Reactive Polymers - Fundamentals and Applications.pdf
Reactive Polymers - Fundamentals and Applications.pdf Reactive Polymers - Fundamentals and Applications.pdf
- Page 2 and 3: REACTIVE POLYMERS FUNDAMENTALS AND
- Page 4 and 5: PDL EDITOR’S PREFACE The publicat
- Page 6 and 7: PREFACE Most of the synthetic polym
- Page 8 and 9: Preface v ACKNOWLEDGEMENTS I am ind
- Page 10 and 11: Chemical Resistance CD-ROM (3 rd Ed
- Page 12 and 13: Contents 1 Unsaturated Polyester Re
- Page 14 and 15: Contents ix 2.5.2 Thermal Propertie
- Page 16 and 17: Contents xi 4.2.5 Production Data o
- Page 18 and 19: Contents xiii References . . . . .
- Page 20 and 21: Contents xv 8.7.4 Electrical Indust
- Page 22 and 23: Contents xvii 11.1.4 Bismaleimide B
- Page 24 and 25: Contents xix 13.4 Properties . . .
- Page 26 and 27: Contents xxi 16.4.7 Sisal Fibers .
- Page 28 and 29: Contents xxiii 18.2.18 Ethyl Diazoa
- Page 30 and 31: 1 Unsaturated Polyester Resins Unsa
- Page 32 and 33: Unsaturated Polyester Resins 3 Satu
- Page 34 and 35: Unsaturated Polyester Resins 5 1.2.
- Page 36 and 37: Unsaturated Polyester Resins 7 O O
- Page 38 and 39: Unsaturated Polyester Resins 9 CH C
- Page 40 and 41: Unsaturated Polyester Resins 11 eth
- Page 42 and 43: Unsaturated Polyester Resins 13 HO
- Page 44 and 45: Unsaturated Polyester Resins 15 O C
- Page 46 and 47: Unsaturated Polyester Resins 17 Tab
- Page 48 and 49: Unsaturated Polyester Resins 19 wax
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REACTIVE POLYMERS<br />
FUNDAMENTALS AND<br />
APPLICATIONS<br />
A CONCISE GUIDE TO INDUSTRIAL POLYMERS<br />
Johannes Karl Fink<br />
Montanuniversität Leoben<br />
Leoben, Austria
Copyright © 2005 by William Andrew, Inc.<br />
No part of this book may be reproduced or utilized in any form or by any means,<br />
electronic or mechanical, including photocopying, recording, or by any information<br />
storage <strong>and</strong> retrieval system, without permission in writing from the Publisher.<br />
Cover art © 2005 by Brent Beckley / William Andrew, Inc.<br />
ISBN: 0-8155-1515-4 (William Andrew, Inc.)<br />
Library or Congress Catalog Card Number: 2005007686<br />
Library of Congress Cataloging-in-Publication Data<br />
Fink, Johannes Karl.<br />
<strong>Reactive</strong> polymers : fundamentals <strong>and</strong> applications : a concise guide to<br />
industrial polymers / by Johannes Karl Fink.<br />
p. cm. -- (PDL h<strong>and</strong>book series)<br />
Includes bibliographical references <strong>and</strong> index.<br />
ISBN 0-8155-1515-4 (acid-free paper)<br />
1. Gums <strong>and</strong> resins, Synthetic. 2. Gums <strong>and</strong> resins--Industrial<br />
applications. I. Title. II. Series.<br />
TP1185.R46F56 2005<br />
668'.374--dc22<br />
2005007686<br />
Printed in the United States of America<br />
This book is printed on acid-free paper.<br />
10 9 8 7 6 5 4 3 2 1<br />
Published by:<br />
William Andrew Publishing<br />
13 Eaton Avenue<br />
Norwich, NY 13815<br />
1-800-932-7045<br />
www.william<strong>and</strong>rew.com<br />
NOTICE<br />
To the best of our knowledge the information in this publication is accurate; however the<br />
Publisher does not assume any responsibility or liability for the accuracy or completeness<br />
of, or consequences arising from, such information. This book is intended for<br />
informational purposes only. Mention of trade names or commercial products does not<br />
constitute endorsement or recommendation for their use by the Publisher. Final<br />
determination of the suitability of any information or product for any use, <strong>and</strong> the manner<br />
of that use, is the sole responsibility of the user. Anyone intending to rely upon any<br />
recommendation of materials or procedures mentioned in this publication should be<br />
independently satisfied as to such suitability, <strong>and</strong> must meet all applicable safety <strong>and</strong><br />
health st<strong>and</strong>ards.
PDL EDITOR’S PREFACE<br />
The publication of <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong>: A<br />
Concise Guide to Industrial <strong>Polymers</strong> in the PDL (Plastics Design Library)<br />
series gives me a special pleasure. The author, Dr. Johannes Karl Fink,<br />
has brought together an impressive array of information about the reactions<br />
polymers undergo, often resulting in cross-linking. The masterful<br />
interweaving of the applications of these reactions with the discussion of<br />
chemistry has rendered this book easy to read for a variety of scientists <strong>and</strong><br />
engineers. The reader learns about the incredible penetration of reactive<br />
plastics into every day life whether in a dentist’s office or an office copier.<br />
On the more cutting edge, the book includes information about carborane<br />
copolymers, which far exceed the temperature resistance of any existing<br />
polymers.<br />
Launched in 1990, the Plastics Design Library (PDL) has established<br />
itself within the materials engineering community as the "go to"<br />
source for information on plastics, elastomers, <strong>and</strong> adhesives. PDL is a<br />
unique series of reference <strong>and</strong> data books essential to the daily work of<br />
practicing engineers <strong>and</strong> scientists in applied industries.<br />
The library encompasses the areas of non-metallic materials with a<br />
special emphasis on plastics, elastomers, coatings, <strong>and</strong> adhesives. Important<br />
current <strong>and</strong> future materials, processing technologies, <strong>and</strong> applications<br />
are emphasized. Future titles are planned in the newer areas of commercial<br />
activity such as nanocomposites, bio-based polymers, recycling <strong>and</strong> mathematical<br />
modeling. The breadth of the coverage ranges from the nature<br />
<strong>and</strong> selection of materials to design <strong>and</strong> fabrication to specification <strong>and</strong><br />
performance.<br />
The uniqueness of PDL is in its balance of practical <strong>and</strong> theoretical<br />
aspects with a clear emphasis of the practical over the theoretical. The<br />
encyclopedic format of the books lends itself to easy reading <strong>and</strong> referral<br />
while the theoretical sections provide the curious reader with an opportunity<br />
for more in-depth learning. Ample references throughout each book<br />
serve as both bibliography <strong>and</strong> additional learning.<br />
Our hope is that this book will meet the needs of people who work<br />
with the reactions of polymers for any reason.<br />
Sina Ebnesajjad<br />
2005<br />
i
ii<br />
Sina Ebnesajjad, Editor Plastics Design Library<br />
Dr. Sina Ebnesajjad is a senior technical consultant at the DuPont Company,<br />
where he has been in a variety of technical assignments since 1982.<br />
Sina is the author of three h<strong>and</strong>books on the science, technology <strong>and</strong> applications<br />
of Fluoroplastics, published by William Andrew, Inc.<br />
He is the Series Editor for the Fluorocarbon H<strong>and</strong>book Series that includes<br />
six h<strong>and</strong>books on fluoroplastics, fluoroelastomers, fluorinated coatings<br />
<strong>and</strong> fluoroionomers. He has been the Editor of Plastics Design Library<br />
since September 2004.
PREFACE<br />
Most of the synthetic polymers are produced in chemical plants <strong>and</strong> delivered<br />
to a plastics manufacturer who does the formulating, blending, extruding<br />
or molding in order to fabricate articles. The processes required for the<br />
final product are purely physical that occur essentially without any chemical<br />
reaction of the polymer. Since most of the polymers are immiscible,<br />
there is not much room to modify the polymer properties during the plastics<br />
manufacturing. The properties of the final product are often modified<br />
by the actions of additives.<br />
A minor number of polymers, usually called resins, are delivered as<br />
precursors by the chemical industry to the manufacturer. Here, the manufacturer<br />
gets to the final article by a chemical reaction. There also exists an<br />
in-between state where polymers can be modified by reactive extrusion <strong>and</strong><br />
grafting. The modification of polymers is advantageous if comparatively<br />
small changes of certain properties are needed that cannot be achieved in<br />
chemical plants. Since many different precursors of the final resin can be<br />
combined, the variability of, <strong>and</strong> thus the ability to modify, the final properties<br />
are much more pronounced in comparison to the rest of polymers.<br />
This is the topic with which the present book deals, namely, chemical<br />
reactions that take place during the final stage of part fabrication from<br />
plastics. The text does not deal with the chemical reactions needed to produce<br />
resin precursors <strong>and</strong> the synthesis of polymers. However, chemical<br />
topics relevant to the part manufacturer are elaborated here. These range<br />
from the manufacture of glass-fiber-reinforced articles such as boats made<br />
by the amateur <strong>and</strong> in a small scale dockyard to what takes place when a<br />
dentist is filling teeth. Industrial processes for the plastics batch fabrication<br />
are described, in addition to their end uses.<br />
The text describes the basic principles of reactive resins as well as<br />
the most recent developments. Paints, coatings <strong>and</strong> adhesives that are constituted<br />
from resins are not dealt with here, even when the curing mechanisms<br />
are similar.<br />
The past art is discussed by reference to monographs, whereas the<br />
recent developments are documented by references in the scientific literature<br />
<strong>and</strong> the patent literature after 2000. In some topics, e.g., urea-formaldehyde<br />
resins, the present research activity is low. In other areas, such<br />
as resins used for nanocomposites, there are many recent papers. Even<br />
those resins, for which the research activity is rather dormant at the moiii
iv<br />
<strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
ment, find widespread use <strong>and</strong> well established applications. They are not<br />
covered here because they are presented in general reviews cited at the beginning<br />
of the respective chapters. Newer applications of these resins are<br />
discussed in detail.<br />
The text originates from a lecture manuscript developed by the author<br />
that has been exp<strong>and</strong>ed into a monograph. The original literature presented<br />
here covers the period until July 2004. The text is at a level that a<br />
chemist with a general eduction in polymer chemistry should underst<strong>and</strong>.<br />
Further, the text is addressed to the advanced student of plastics engineering<br />
<strong>and</strong> the practicing engineer.<br />
HOW TO USE THIS BOOK<br />
Utmost care has been taken to present reliable data. Because of the vast<br />
variety of material presented here, however, it cannot be complete in all<br />
relevant aspects, <strong>and</strong> it is recommended that the reader study the original<br />
literature for complete information. Therefore, the author cannot assume<br />
responsibility for the completeness <strong>and</strong> validity of, nor for the consequences<br />
of, the use of the material presented here. Every attempt was made<br />
to identify trademarked products in this volume; however, there were some<br />
that the author was unable to locate, <strong>and</strong> we apologize for any inadvertent<br />
omission.<br />
Index<br />
There are three indices: an index of acronyms, an index of chemicals, <strong>and</strong><br />
a general index. Unfortunately the acronyms presented in the literature are<br />
not always consistent. This means that in a few cases the same acronym<br />
st<strong>and</strong>s for different terms.<br />
Further, in the literature the acronyms are sometimes exp<strong>and</strong>ed in<br />
a different way, in particular for chemical names. The author has not unified<br />
the system of chemical names, even when the same compound appears<br />
with different names, because otherwise back tracing in the original literature<br />
would be difficult. I apologize here for this somewhat unsatisfactory<br />
situation.<br />
In the index of chemicals, compounds that occur extensively, e.g.,<br />
“styrene”, are not included at every occurrence, but rather when they appear<br />
in an important context.
Preface<br />
v<br />
ACKNOWLEDGEMENTS<br />
I am indebted to our local library, Dr. Lieselotte Jontes, Dr. Johann Delanoy,<br />
Franz Jurek, Friedrich Scheer, <strong>and</strong> Christian Slamenik for support in<br />
literature acquisition. I express my gratitude to all the scientists who have<br />
carefully published their results concerning the topics dealt with here. The<br />
book could not have been compiled otherwise.<br />
I would like to thank Dr. Sina Ebnesajjad, Editor of Plastics Design<br />
Library (PDL) for his review <strong>and</strong> comments on the manuscript. The<br />
Editorial Staff of William Andrew, Inc. have been most supportive of this<br />
project, especially Ms. Millicent Treloar, Senior Acquisitions Editor, who<br />
has been tireless in her efforts. Thank you Ms. Joan Bally for copy editing<br />
the manuscript.<br />
J. K. F.
Plastics Design Library<br />
PDL Editor: Sina Ebnesajjad<br />
Founding Editor: William A. Woishnis<br />
Fluoroelastomers <strong>Applications</strong> in Chemical Processing Industries<br />
ISBN: 0-8155-1502-2<br />
Khaladkar, P. R., Ebnesajjad, S., Pub. Date: 2005, 592 Pages<br />
The Effect of Sterilization Methods on Plastics <strong>and</strong> Elastomers, 2 nd Ed.<br />
ISBN: 0-8155-1505-7<br />
Massey, L. K., Pub. Date: 2005, 408 Pages<br />
Extrusion: The Definitive Processing Guide <strong>and</strong> H<strong>and</strong>book<br />
ISBN: 0-8155-1473-5<br />
Giles, H. F., Jr., Wagner,J. R., Jr., Mount, E. M., III, Pub. Date: 2005, 572 Pages<br />
Film Properties of Plastics <strong>and</strong> Elastomers, 2 nd Ed.<br />
ISBN 1-884207-94-4<br />
Massey, L. K., Pub. Date: 2004, 250 Pages<br />
H<strong>and</strong>book of Molded Part Shrinkage <strong>and</strong> Warpage<br />
ISBN 1-884207-72-3<br />
Fischer, J., Pub. Date: 2003, 244 Pages<br />
Fluoroplastics, Volume 2: Melt-Processible Fluoroplastics<br />
ISBN 1-884207-96-0<br />
Ebnesajjad, S., Pub. Date: 2002, 448 Pages<br />
Permeability Properties of Plastics <strong>and</strong> Elastomers, 2 nd Ed.<br />
ISBN 1-884207-97-9<br />
Massey, L. K., Pub. Date: 2002, 550 Pages<br />
Rotational Molding Technology<br />
ISBN 1-884207-85-5<br />
Crawford, R. J., <strong>and</strong> Throne, J. L. , Pub. Date: 2002, 450 Pages<br />
Specialized Molding Techniques & Application, Design, Materials <strong>and</strong> Processing<br />
ISBN 1-884207-91-X<br />
Heim, H. P., <strong>and</strong> Potente, H., Pub. Date: 2002, 350 Pages
Chemical Resistance CD-ROM (3 rd Ed.)<br />
ISBN 1-884207-90-1<br />
Plastics Design Library Staff, Pub. Date: 2001, CD-rom<br />
Plastics Failure Analysis <strong>and</strong> Prevention<br />
ISBN 1-884207-92-8<br />
Moalli, J., Pub. Date: 2001, 400 Pages<br />
Fluoroplastics, Volume 1: Non-Melt Processible Fluoroplastics<br />
ISBN 1-884207-84-7<br />
Ebnesajjad, S., Pub. Date: 2000, 365 Pages<br />
Coloring Technology for Plastics<br />
ISBN 1-884207-78-2<br />
Harris, R. M., Pub. Date: 1999, 333 Pages<br />
Conductive <strong>Polymers</strong> <strong>and</strong> Plastics in Industrial <strong>Applications</strong><br />
ISBN 1-884207-77-4<br />
Rupprecht, L. M., Pub. Date: 1999, 302 Pages<br />
Imaging <strong>and</strong> Image Analysis <strong>Applications</strong> for Plastics<br />
ISBN 1-884207-81-2<br />
Pourdeyhimi, B., Pub. Date: 1999, 398 Pages<br />
Metallocene Technology in Commercial <strong>Applications</strong><br />
ISBN 1-884207-76-6<br />
Benedikt, G. M., Pub. Date: 1999, 325 Pages<br />
Weathering of Plastics<br />
ISBN 1-884207-75-8<br />
Wypych, G., Pub. Date: 1999, 325 Pages<br />
Dynamic Mechanical Analysis for Plastics Engineering<br />
ISBN 1-884207-64-2<br />
Sepe, M.. Pub. Date: 1998, 230 Pages<br />
Medical Plastics: Degradation Resistance <strong>and</strong> Failure Analysis<br />
ISBN 1-884207-60-X<br />
Portnoy, R. C., Pub. Date: 1998, 215 Pages
Metallocene Catalyzed <strong>Polymers</strong><br />
ISBN 1-884207-59-6<br />
Benedikt, G. M., <strong>and</strong> Goodall, B. L., Pub. Date: 1998, 400 Pages<br />
Polypropylene: The Definitive User’s Guide <strong>and</strong> Databook<br />
ISBN 1-884207-58-8<br />
Maier, C., <strong>and</strong> Calafut, T., Pub. Date: 1998, 425 Pages<br />
H<strong>and</strong>book of Plastics Joining<br />
ISBN 1-884207-17-0<br />
Plastics Design Library Staff, Pub. Date: 1997, 600 Pages<br />
Fatigue <strong>and</strong> Tribological Properties of Plastics <strong>and</strong> Elastomers<br />
ISBN 1-884207-15-4<br />
Plastics Design Library Staff, Pub. Date: 1995, 595 Pages<br />
Chemical Resistance, Volume 1<br />
ISBN 1-884207-12-X<br />
Plastics Design Library Staff, Pub. Date: 1994, 1100 Pages<br />
Chemical Resistance, Volume 2<br />
ISBN 1-884207-13-8<br />
Plastics Design Library Staff, Pub. Date: 1994, 977 Pages<br />
The Effect of UV Light <strong>and</strong> Weather on Plastics <strong>and</strong> Elastomers<br />
ISBN 1-884207-11-1<br />
Plastics Design Library Staff, Pub. Date: 1994, 481 Pages<br />
The Effect of Creep <strong>and</strong> Other Time Related<br />
Factors on Plastics <strong>and</strong> Elastomers<br />
ISBN 1-884207-03-0<br />
Plastics Design Library Staff, Pub. Date: 1991, 528 Pages<br />
The Effect of Temperature <strong>and</strong> Other Factors on Plastics<br />
ISBN 1-884207-06-5<br />
Plastics Design Library Staff, Pub. Date: 1991, 420 Pages
Contents<br />
1 Unsaturated Polyester Resins 1<br />
1.1 History . . . . . . . . . . . . . . . . . . . . . . . . . . 1<br />
1.2 Monomers . . . . . . . . . . . . . . . . . . . . . . . . . 2<br />
1.2.1 Monomers for the Unsaturated Polyester (UP) . 2<br />
1.2.2 Vinyl Monomers . . . . . . . . . . . . . . . . . 8<br />
1.2.3 Specialities . . . . . . . . . . . . . . . . . . . . 10<br />
1.2.4 Synthesis . . . . . . . . . . . . . . . . . . . . . 13<br />
1.2.5 Manufacture . . . . . . . . . . . . . . . . . . . 15<br />
1.3 Special Additives . . . . . . . . . . . . . . . . . . . . . 17<br />
1.3.1 Inhibitors . . . . . . . . . . . . . . . . . . . . . 17<br />
1.3.2 Thickeners . . . . . . . . . . . . . . . . . . . . 18<br />
1.3.3 Emission Suppressants . . . . . . . . . . . . . . 18<br />
1.3.4 Fillers . . . . . . . . . . . . . . . . . . . . . . . 19<br />
1.3.5 Reinforcing Materials . . . . . . . . . . . . . . 23<br />
1.3.6 Mold Release Agents . . . . . . . . . . . . . . . 25<br />
1.3.7 Low-profile Additives . . . . . . . . . . . . . . 26<br />
1.3.8 Interpenetrating Polymer Networks . . . . . . . 28<br />
1.3.9 Polyurethane Hybrid Networks . . . . . . . . . 30<br />
1.3.10 Flame Retardants . . . . . . . . . . . . . . . . . 31<br />
1.3.11 Production Data . . . . . . . . . . . . . . . . . 34<br />
1.4 Curing . . . . . . . . . . . . . . . . . . . . . . . . . . . 34<br />
1.4.1 Initiator Systems . . . . . . . . . . . . . . . . . 35<br />
1.4.2 Promoters . . . . . . . . . . . . . . . . . . . . . 37<br />
1.4.3 Initiator Promoter Systems . . . . . . . . . . . . 40<br />
1.4.4 Polymerization . . . . . . . . . . . . . . . . . . 40<br />
1.5 Properties . . . . . . . . . . . . . . . . . . . . . . . . . 44<br />
vii
viii<br />
<strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
1.5.1 Structure Properties Relationships . . . . . . . . 44<br />
1.5.2 Hydrolytic Stability . . . . . . . . . . . . . . . 45<br />
1.5.3 Recycling . . . . . . . . . . . . . . . . . . . . . 45<br />
1.6 <strong>Applications</strong> <strong>and</strong> Uses . . . . . . . . . . . . . . . . . . 46<br />
1.6.1 Decorative Specimens . . . . . . . . . . . . . . 47<br />
1.6.2 Polyester Concrete . . . . . . . . . . . . . . . . 47<br />
1.6.3 Reinforced Materials . . . . . . . . . . . . . . . 47<br />
1.6.4 Coatings . . . . . . . . . . . . . . . . . . . . . 48<br />
1.7 Special Formulations . . . . . . . . . . . . . . . . . . . 49<br />
1.7.1 Electrically Conductive Resins . . . . . . . . . . 50<br />
1.7.2 Fluoro Copolymers . . . . . . . . . . . . . . . . 50<br />
1.7.3 Toner Compositions . . . . . . . . . . . . . . . 51<br />
1.7.4 Pour Point Depressants . . . . . . . . . . . . . . 52<br />
1.7.5 Biodegradable Polyesters . . . . . . . . . . . . 52<br />
1.7.6 Bone Cement . . . . . . . . . . . . . . . . . . . 52<br />
1.7.7 Compatibilizers . . . . . . . . . . . . . . . . . . 53<br />
1.7.8 <strong>Reactive</strong> Melt Modification of Poly(propylene) . 53<br />
References . . . . . . . . . . . . . . . . . . . . . . . . . . . . 53<br />
2 Polyurethanes 69<br />
2.1 History . . . . . . . . . . . . . . . . . . . . . . . . . . 69<br />
2.2 Monomers . . . . . . . . . . . . . . . . . . . . . . . . . 70<br />
2.2.1 Diisocyanates . . . . . . . . . . . . . . . . . . . 70<br />
2.2.2 Polyols . . . . . . . . . . . . . . . . . . . . . . 84<br />
2.2.3 Other Polyols . . . . . . . . . . . . . . . . . . . 90<br />
2.2.4 Polyamines . . . . . . . . . . . . . . . . . . . . 91<br />
2.2.5 Chain Extenders . . . . . . . . . . . . . . . . . 92<br />
2.2.6 Catalysts . . . . . . . . . . . . . . . . . . . . . 92<br />
2.2.7 Blowing . . . . . . . . . . . . . . . . . . . . . 94<br />
2.3 Special Additives . . . . . . . . . . . . . . . . . . . . . 109<br />
2.3.1 Fillers . . . . . . . . . . . . . . . . . . . . . . . 109<br />
2.3.2 Reinforcing Materials . . . . . . . . . . . . . . 110<br />
2.3.3 Flame Retardants . . . . . . . . . . . . . . . . . 111<br />
2.3.4 Production Data . . . . . . . . . . . . . . . . . 113<br />
2.4 Curing . . . . . . . . . . . . . . . . . . . . . . . . . . . 114<br />
2.4.1 Recycling . . . . . . . . . . . . . . . . . . . . . 114<br />
2.5 Properties . . . . . . . . . . . . . . . . . . . . . . . . . 115<br />
2.5.1 Mechanical Properties . . . . . . . . . . . . . . 115
Contents<br />
ix<br />
2.5.2 Thermal Properties . . . . . . . . . . . . . . . . 116<br />
2.5.3 Weathering Resistance . . . . . . . . . . . . . . 116<br />
2.6 <strong>Applications</strong> <strong>and</strong> Uses . . . . . . . . . . . . . . . . . . 116<br />
2.6.1 Casting . . . . . . . . . . . . . . . . . . . . . . 116<br />
2.7 Special Formulations . . . . . . . . . . . . . . . . . . . 117<br />
2.7.1 Interpenetrating Networks . . . . . . . . . . . . 117<br />
2.7.2 Grafting with Isocyanates . . . . . . . . . . . . 118<br />
2.7.3 Medical <strong>Applications</strong> . . . . . . . . . . . . . . . 118<br />
2.7.4 Waterborne Polyurethanes . . . . . . . . . . . . 120<br />
2.7.5 Ceramic Foams . . . . . . . . . . . . . . . . . . 122<br />
2.7.6 Adhesion Modification . . . . . . . . . . . . . . 122<br />
2.7.7 Electrolytes . . . . . . . . . . . . . . . . . . . . 122<br />
References . . . . . . . . . . . . . . . . . . . . . . . . . . . . 124<br />
3 Epoxy Resins 139<br />
3.1 History . . . . . . . . . . . . . . . . . . . . . . . . . . 139<br />
3.2 Monomers . . . . . . . . . . . . . . . . . . . . . . . . . 139<br />
3.2.1 Epoxides . . . . . . . . . . . . . . . . . . . . . 139<br />
3.2.2 Phenols . . . . . . . . . . . . . . . . . . . . . . 140<br />
3.2.3 Specialities . . . . . . . . . . . . . . . . . . . . 144<br />
3.2.4 Manufacture . . . . . . . . . . . . . . . . . . . 146<br />
3.3 Special Additives . . . . . . . . . . . . . . . . . . . . . 151<br />
3.3.1 Toughening Agents . . . . . . . . . . . . . . . . 151<br />
3.3.2 Antiplasticizers . . . . . . . . . . . . . . . . . . 159<br />
3.3.3 Lubricants . . . . . . . . . . . . . . . . . . . . 160<br />
3.3.4 Adhesion Improvers . . . . . . . . . . . . . . . 160<br />
3.3.5 Conductivity Modifiers . . . . . . . . . . . . . . 161<br />
3.3.6 Reinforcing Materials . . . . . . . . . . . . . . 161<br />
3.3.7 Interpenetrating Polymer Networks . . . . . . . 164<br />
3.3.8 Organic <strong>and</strong> Inorganic Hybrids . . . . . . . . . 167<br />
3.3.9 Flame Retardants . . . . . . . . . . . . . . . . . 168<br />
3.3.10 Production Data . . . . . . . . . . . . . . . . . 173<br />
3.4 Curing . . . . . . . . . . . . . . . . . . . . . . . . . . . 173<br />
3.4.1 Initiator Systems . . . . . . . . . . . . . . . . . 173<br />
3.4.2 Compounds with Activated Hydrogen . . . . . . 174<br />
3.4.3 Coordination Catalysts . . . . . . . . . . . . . . 182<br />
3.4.4 Ionic Curing . . . . . . . . . . . . . . . . . . . 183<br />
3.4.5 Photoinitiators . . . . . . . . . . . . . . . . . . 186
x<br />
<strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
3.4.6 Derivatives of Michler’s Ketone . . . . . . . . . 189<br />
3.4.7 Epoxy Systems with Vinyl Groups . . . . . . . . 193<br />
3.4.8 Curing Kinetics . . . . . . . . . . . . . . . . . . 193<br />
3.4.9 Thermal Curing . . . . . . . . . . . . . . . . . 197<br />
3.4.10 Microwave Curing . . . . . . . . . . . . . . . . 197<br />
3.5 Properties . . . . . . . . . . . . . . . . . . . . . . . . . 198<br />
3.5.1 Hybrid <strong>Polymers</strong> <strong>and</strong> Mixed <strong>Polymers</strong> . . . . . 199<br />
3.5.2 Recycling . . . . . . . . . . . . . . . . . . . . . 200<br />
3.6 <strong>Applications</strong> <strong>and</strong> Uses . . . . . . . . . . . . . . . . . . 203<br />
3.6.1 Coatings . . . . . . . . . . . . . . . . . . . . . 203<br />
3.6.2 Foams . . . . . . . . . . . . . . . . . . . . . . 203<br />
3.6.3 Adhesives . . . . . . . . . . . . . . . . . . . . . 203<br />
3.6.4 Molding Techniques . . . . . . . . . . . . . . . 203<br />
3.6.5 Stabilizers for Polyvinyl Chloride . . . . . . . . 204<br />
3.7 Special Formulations . . . . . . . . . . . . . . . . . . . 204<br />
3.7.1 Development of Formulations . . . . . . . . . . 204<br />
3.7.2 Restoration Materials . . . . . . . . . . . . . . . 205<br />
3.7.3 Biodegradable Epoxy-polyester Resins . . . . . 205<br />
3.7.4 Swellable Epoxies . . . . . . . . . . . . . . . . 205<br />
3.7.5 <strong>Reactive</strong> Membrane Materials . . . . . . . . . . 206<br />
3.7.6 Controlled-release Formulations for Agriculture 206<br />
3.7.7 Electronic Packaging Application . . . . . . . . 206<br />
3.7.8 Solid Polymer Electrolytes . . . . . . . . . . . . 207<br />
3.7.9 Optical Resins . . . . . . . . . . . . . . . . . . 207<br />
3.7.10 <strong>Reactive</strong> Solvents . . . . . . . . . . . . . . . . . 210<br />
3.7.11 Encapsulated Systems . . . . . . . . . . . . . . 211<br />
3.7.12 Functionalized <strong>Polymers</strong> . . . . . . . . . . . . . 212<br />
3.7.13 Epoxy Resins as Compatibilizers . . . . . . . . 212<br />
3.7.14 Surface Metallization . . . . . . . . . . . . . . . 215<br />
References . . . . . . . . . . . . . . . . . . . . . . . . . . . . 215<br />
4 Phenol/formaldehyde Resins 241<br />
4.1 History . . . . . . . . . . . . . . . . . . . . . . . . . . 242<br />
4.2 Monomers . . . . . . . . . . . . . . . . . . . . . . . . . 243<br />
4.2.1 Phenol . . . . . . . . . . . . . . . . . . . . . . 244<br />
4.2.2 o-Cresol . . . . . . . . . . . . . . . . . . . . . 244<br />
4.2.3 Formaldehyde . . . . . . . . . . . . . . . . . . 245<br />
4.2.4 Multihydroxymethylketones . . . . . . . . . . . 246
Contents<br />
xi<br />
4.2.5 Production Data of Important Monomers . . . . 246<br />
4.2.6 Basic Resin Types . . . . . . . . . . . . . . . . 247<br />
4.2.7 Specialities . . . . . . . . . . . . . . . . . . . . 247<br />
4.2.8 Synthesis . . . . . . . . . . . . . . . . . . . . . 249<br />
4.2.9 Catalysts . . . . . . . . . . . . . . . . . . . . . 251<br />
4.2.10 Manufacture . . . . . . . . . . . . . . . . . . . 254<br />
4.3 Special Additives . . . . . . . . . . . . . . . . . . . . . 255<br />
4.3.1 Low Emission Types . . . . . . . . . . . . . . . 255<br />
4.3.2 Boric Acid-modified Types . . . . . . . . . . . 257<br />
4.3.3 Fillers . . . . . . . . . . . . . . . . . . . . . . . 259<br />
4.3.4 Flame Retardants . . . . . . . . . . . . . . . . . 259<br />
4.4 Curing . . . . . . . . . . . . . . . . . . . . . . . . . . . 260<br />
4.4.1 Model Studies . . . . . . . . . . . . . . . . . . 260<br />
4.4.2 Experimental Design . . . . . . . . . . . . . . . 261<br />
4.4.3 Water Content . . . . . . . . . . . . . . . . . . 262<br />
4.4.4 Influence of Pressure . . . . . . . . . . . . . . . 262<br />
4.4.5 Wood . . . . . . . . . . . . . . . . . . . . . . . 262<br />
4.4.6 Novolak Curing Agents . . . . . . . . . . . . . 262<br />
4.4.7 Resol Resin Hardeners . . . . . . . . . . . . . . 263<br />
4.4.8 Ester-type Accelerators . . . . . . . . . . . . . . 264<br />
4.4.9 Ashless Resol Resins . . . . . . . . . . . . . . . 264<br />
4.4.10 Recycling . . . . . . . . . . . . . . . . . . . . . 265<br />
4.5 <strong>Applications</strong> <strong>and</strong> Uses . . . . . . . . . . . . . . . . . . 266<br />
4.5.1 Binders for Glass Fibers . . . . . . . . . . . . . 266<br />
4.5.2 Molding . . . . . . . . . . . . . . . . . . . . . 268<br />
4.5.3 Novolak Photoresists . . . . . . . . . . . . . . . 268<br />
4.5.4 High Temperature Adhesives . . . . . . . . . . 269<br />
4.5.5 Urethane-modified Types . . . . . . . . . . . . 269<br />
4.5.6 Carbon Products . . . . . . . . . . . . . . . . . 270<br />
4.6 Special Formulations . . . . . . . . . . . . . . . . . . . 272<br />
4.6.1 Chemical Resistant Types . . . . . . . . . . . . 272<br />
4.6.2 Ion Exchange Resins . . . . . . . . . . . . . . . 272<br />
4.6.3 Brakes . . . . . . . . . . . . . . . . . . . . . . 273<br />
4.6.4 Waterborne Types . . . . . . . . . . . . . . . . 273<br />
4.6.5 High Viscosity Novolak . . . . . . . . . . . . . 273<br />
4.6.6 Foams . . . . . . . . . . . . . . . . . . . . . . 273<br />
4.6.7 Visbreaking of Petroleum . . . . . . . . . . . . 274<br />
4.7 Testing Methods . . . . . . . . . . . . . . . . . . . . . . 274
xii<br />
<strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
4.7.1 Water Tolerance . . . . . . . . . . . . . . . . . 274<br />
4.7.2 Salt Tolerance . . . . . . . . . . . . . . . . . . 274<br />
4.7.3 Free Phenol Content . . . . . . . . . . . . . . . 275<br />
4.7.4 Free Formaldehyde . . . . . . . . . . . . . . . . 275<br />
4.7.5 pH . . . . . . . . . . . . . . . . . . . . . . . . 275<br />
4.7.6 Solids Content . . . . . . . . . . . . . . . . . . 275<br />
4.7.7 o-Cresol Contact Allergy . . . . . . . . . . . . . 275<br />
References . . . . . . . . . . . . . . . . . . . . . . . . . . . . 275<br />
5 Urea/formaldehyde Resins 283<br />
5.1 History . . . . . . . . . . . . . . . . . . . . . . . . . . 283<br />
5.2 Synthesis of Resin . . . . . . . . . . . . . . . . . . . . . 283<br />
5.2.1 Formaldehyde . . . . . . . . . . . . . . . . . . 283<br />
5.2.2 Urea . . . . . . . . . . . . . . . . . . . . . . . 284<br />
5.2.3 Ammonia . . . . . . . . . . . . . . . . . . . . . 284<br />
5.2.4 Diketones . . . . . . . . . . . . . . . . . . . . . 284<br />
5.2.5 Specialities . . . . . . . . . . . . . . . . . . . . 284<br />
5.2.6 Polymerization . . . . . . . . . . . . . . . . . . 286<br />
5.2.7 Manufacture . . . . . . . . . . . . . . . . . . . 290<br />
5.3 Special Additives . . . . . . . . . . . . . . . . . . . . . 290<br />
5.3.1 Modifiers . . . . . . . . . . . . . . . . . . . . . 290<br />
5.3.2 Flame Retardants . . . . . . . . . . . . . . . . . 291<br />
5.3.3 Production Data of Important Monomers . . . . 291<br />
5.4 Curing . . . . . . . . . . . . . . . . . . . . . . . . . . . 291<br />
5.5 Measurement of Curing . . . . . . . . . . . . . . . . . . 292<br />
5.6 Properties . . . . . . . . . . . . . . . . . . . . . . . . . 293<br />
5.6.1 Formaldehyde Release . . . . . . . . . . . . . . 293<br />
5.6.2 Storage . . . . . . . . . . . . . . . . . . . . . . 293<br />
5.7 <strong>Applications</strong> <strong>and</strong> Uses . . . . . . . . . . . . . . . . . . 294<br />
5.7.1 Glue Resins . . . . . . . . . . . . . . . . . . . . 294<br />
5.7.2 Binders . . . . . . . . . . . . . . . . . . . . . . 294<br />
5.7.3 Foundry S<strong>and</strong>s . . . . . . . . . . . . . . . . . . 294<br />
5.8 Special Formulations . . . . . . . . . . . . . . . . . . . 294<br />
5.8.1 Ready-use Powders . . . . . . . . . . . . . . . . 294<br />
5.8.2 Cyclic Urea Prepolymer in PF Laminating Resins 295<br />
5.8.3 Liquid Fertilizer . . . . . . . . . . . . . . . . . 295<br />
5.8.4 Soil Amendment . . . . . . . . . . . . . . . . . 295<br />
5.8.5 Microencapsulation . . . . . . . . . . . . . . . 296
Contents<br />
xiii<br />
References . . . . . . . . . . . . . . . . . . . . . . . . . . . . 296<br />
6 Melamine Resins 299<br />
6.1 History . . . . . . . . . . . . . . . . . . . . . . . . . . 299<br />
6.2 Monomers . . . . . . . . . . . . . . . . . . . . . . . . . 299<br />
6.2.1 Melamine . . . . . . . . . . . . . . . . . . . . . 299<br />
6.2.2 Other Modifiers . . . . . . . . . . . . . . . . . 300<br />
6.2.3 Synthesis . . . . . . . . . . . . . . . . . . . . . 300<br />
6.2.4 Manufacture . . . . . . . . . . . . . . . . . . . 302<br />
6.3 Properties . . . . . . . . . . . . . . . . . . . . . . . . . 302<br />
6.4 <strong>Applications</strong> <strong>and</strong> Uses . . . . . . . . . . . . . . . . . . 303<br />
6.4.1 Wood Impregnation . . . . . . . . . . . . . . . 303<br />
6.5 Special Formulations . . . . . . . . . . . . . . . . . . . 304<br />
6.5.1 Resins with Increased Elasticity . . . . . . . . . 304<br />
6.5.2 Microspheres . . . . . . . . . . . . . . . . . . . 304<br />
References . . . . . . . . . . . . . . . . . . . . . . . . . . . . 304<br />
7 Furan Resins 307<br />
7.1 History . . . . . . . . . . . . . . . . . . . . . . . . . . 307<br />
7.2 Monomers . . . . . . . . . . . . . . . . . . . . . . . . . 307<br />
7.2.1 Furfural . . . . . . . . . . . . . . . . . . . . . . 308<br />
7.2.2 Furfuryl Alcohol . . . . . . . . . . . . . . . . . 309<br />
7.2.3 Specialities . . . . . . . . . . . . . . . . . . . . 309<br />
7.2.4 Synthesis . . . . . . . . . . . . . . . . . . . . . 309<br />
7.3 Special Additives . . . . . . . . . . . . . . . . . . . . . 310<br />
7.3.1 Reinforcing Materials . . . . . . . . . . . . . . 310<br />
7.3.2 Production Data of Important Monomers . . . . 311<br />
7.4 Curing . . . . . . . . . . . . . . . . . . . . . . . . . . . 311<br />
7.4.1 Acidic Curing . . . . . . . . . . . . . . . . . . 312<br />
7.4.2 Oxidative Curing . . . . . . . . . . . . . . . . . 312<br />
7.4.3 Ultrasonic Curing . . . . . . . . . . . . . . . . 312<br />
7.5 Properties . . . . . . . . . . . . . . . . . . . . . . . . . 313<br />
7.5.1 Recycling . . . . . . . . . . . . . . . . . . . . . 313<br />
7.6 <strong>Applications</strong> <strong>and</strong> Uses . . . . . . . . . . . . . . . . . . 313<br />
7.6.1 Carbons . . . . . . . . . . . . . . . . . . . . . . 313<br />
7.6.2 Chromatography Support . . . . . . . . . . . . 314<br />
7.6.3 Composite Carbon Fiber Materials . . . . . . . 315<br />
7.6.4 Foundry Binders . . . . . . . . . . . . . . . . . 316<br />
7.6.5 Glass Fiber Binders . . . . . . . . . . . . . . . 316
xiv<br />
<strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
7.6.6 Oil Field <strong>Applications</strong> . . . . . . . . . . . . . . 317<br />
7.6.7 Plant Growth Substrates . . . . . . . . . . . . . 317<br />
7.6.8 Photosensitive Polymer Electrolytes . . . . . . . 317<br />
References . . . . . . . . . . . . . . . . . . . . . . . . . . . . 319<br />
8 Silicones 321<br />
8.1 History . . . . . . . . . . . . . . . . . . . . . . . . . . 321<br />
8.2 Monomers . . . . . . . . . . . . . . . . . . . . . . . . . 322<br />
8.2.1 Chlorosilanes . . . . . . . . . . . . . . . . . . . 322<br />
8.2.2 Silsesquioxanes . . . . . . . . . . . . . . . . . . 322<br />
8.2.3 Hydrogen Silsesquioxanes . . . . . . . . . . . . 322<br />
8.2.4 Alkoxy Siloxanes . . . . . . . . . . . . . . . . . 324<br />
8.2.5 Epoxy-modified Siloxanes . . . . . . . . . . . . 325<br />
8.2.6 Silaferrocenophanes . . . . . . . . . . . . . . . 325<br />
8.2.7 Synthesis . . . . . . . . . . . . . . . . . . . . . 327<br />
8.2.8 Manufacture . . . . . . . . . . . . . . . . . . . 330<br />
8.3 Modified Types . . . . . . . . . . . . . . . . . . . . . . 331<br />
8.3.1 Chemical Modifications . . . . . . . . . . . . . 331<br />
8.3.2 Fillers . . . . . . . . . . . . . . . . . . . . . . . 331<br />
8.3.3 Reinforcing Materials . . . . . . . . . . . . . . 332<br />
8.4 Curing . . . . . . . . . . . . . . . . . . . . . . . . . . . 332<br />
8.4.1 Curing by Condensation . . . . . . . . . . . . . 332<br />
8.5 Crosslinking . . . . . . . . . . . . . . . . . . . . . . . . 334<br />
8.5.1 Condensation Crosslinking . . . . . . . . . . . . 334<br />
8.5.2 Peroxides . . . . . . . . . . . . . . . . . . . . . 335<br />
8.5.3 Hydrosilylation Crosslinking . . . . . . . . . . . 335<br />
8.6 Properties . . . . . . . . . . . . . . . . . . . . . . . . . 336<br />
8.6.1 Silicone Rubber . . . . . . . . . . . . . . . . . 336<br />
8.6.2 Thermal Properties . . . . . . . . . . . . . . . . 336<br />
8.6.3 Electrical Properties . . . . . . . . . . . . . . . 338<br />
8.6.4 Surface Tension Properties . . . . . . . . . . . . 338<br />
8.6.5 Antioxidants . . . . . . . . . . . . . . . . . . . 338<br />
8.6.6 Gas Permeability . . . . . . . . . . . . . . . . . 338<br />
8.6.7 Weathering . . . . . . . . . . . . . . . . . . . . 340<br />
8.7 <strong>Applications</strong> <strong>and</strong> Uses . . . . . . . . . . . . . . . . . . 340<br />
8.7.1 Antifoaming Agents . . . . . . . . . . . . . . . 340<br />
8.7.2 Release Agents . . . . . . . . . . . . . . . . . . 340<br />
8.7.3 Sealing <strong>and</strong> Jointing Materials . . . . . . . . . . 341
Contents<br />
xv<br />
8.7.4 Electrical Industry . . . . . . . . . . . . . . . . 341<br />
8.7.5 Medical <strong>Applications</strong> . . . . . . . . . . . . . . . 341<br />
8.8 Special Formulations . . . . . . . . . . . . . . . . . . . 342<br />
8.8.1 Polyimide Resins . . . . . . . . . . . . . . . . . 342<br />
8.8.2 Thermal Transfer Ribbons . . . . . . . . . . . . 342<br />
8.8.3 Self-Assembly Systems . . . . . . . . . . . . . 343<br />
8.8.4 Plasma Grafting . . . . . . . . . . . . . . . . . 343<br />
8.8.5 Antifouling Compositions . . . . . . . . . . . . 344<br />
References . . . . . . . . . . . . . . . . . . . . . . . . . . . . 345<br />
9 Acrylic Resins 349<br />
9.1 History . . . . . . . . . . . . . . . . . . . . . . . . . . 349<br />
9.2 Monomers . . . . . . . . . . . . . . . . . . . . . . . . . 350<br />
9.2.1 Specialities . . . . . . . . . . . . . . . . . . . . 350<br />
9.2.2 Synthesis . . . . . . . . . . . . . . . . . . . . . 352<br />
9.2.3 Manufacture . . . . . . . . . . . . . . . . . . . 353<br />
9.3 Special Additives . . . . . . . . . . . . . . . . . . . . . 356<br />
9.3.1 Ultraviolet Absorbers . . . . . . . . . . . . . . 356<br />
9.3.2 Flame Retardants . . . . . . . . . . . . . . . . . 356<br />
9.3.3 Production Data of Important Monomers . . . . 358<br />
9.4 Curing . . . . . . . . . . . . . . . . . . . . . . . . . . . 358<br />
9.4.1 Initiator Systems . . . . . . . . . . . . . . . . . 358<br />
9.4.2 Promoters . . . . . . . . . . . . . . . . . . . . . 360<br />
9.5 Properties . . . . . . . . . . . . . . . . . . . . . . . . . 360<br />
9.5.1 Electrical Properties . . . . . . . . . . . . . . . 360<br />
9.5.2 Hydrolytic <strong>and</strong> Photochemical Stability . . . . . 361<br />
9.5.3 Recycling . . . . . . . . . . . . . . . . . . . . . 361<br />
9.6 <strong>Applications</strong> <strong>and</strong> Uses . . . . . . . . . . . . . . . . . . 361<br />
9.6.1 Acrylic Premixes . . . . . . . . . . . . . . . . . 361<br />
9.6.2 Protective Coatings in Electronic Devices . . . . 362<br />
9.6.3 High-performance Biocomposite . . . . . . . . 363<br />
9.6.4 Solid Polymer Electrolytes . . . . . . . . . . . . 363<br />
9.7 Special Formulations . . . . . . . . . . . . . . . . . . . 365<br />
9.7.1 Silane <strong>and</strong> Siloxane Acrylate Resins . . . . . . . 365<br />
9.7.2 Marble Conservation . . . . . . . . . . . . . . . 365<br />
9.7.3 Tackifier Resins . . . . . . . . . . . . . . . . . 366<br />
9.7.4 Drug Release Membranes . . . . . . . . . . . . 366<br />
9.7.5 Support Materials for Catalysts . . . . . . . . . 367
xvi<br />
<strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
9.7.6 Electron Microscopy . . . . . . . . . . . . . . . 367<br />
9.7.7 Stereolithography . . . . . . . . . . . . . . . . 367<br />
9.7.8 Laminated Films . . . . . . . . . . . . . . . . . 367<br />
9.7.9 Ink-jet Printing Media . . . . . . . . . . . . . . 368<br />
References . . . . . . . . . . . . . . . . . . . . . . . . . . . . 369<br />
10 Cyanate Ester Resins 373<br />
10.1 History . . . . . . . . . . . . . . . . . . . . . . . . . . 373<br />
10.2 Monomers . . . . . . . . . . . . . . . . . . . . . . . . . 373<br />
10.2.1 Specialities . . . . . . . . . . . . . . . . . . . . 373<br />
10.2.2 Synthesis . . . . . . . . . . . . . . . . . . . . . 375<br />
10.3 Special Additives . . . . . . . . . . . . . . . . . . . . . 377<br />
10.3.1 Fillers . . . . . . . . . . . . . . . . . . . . . . . 377<br />
10.3.2 Flame Retardants . . . . . . . . . . . . . . . . . 378<br />
10.4 Curing . . . . . . . . . . . . . . . . . . . . . . . . . . . 379<br />
10.4.1 Thermal Curing . . . . . . . . . . . . . . . . . 379<br />
10.4.2 Curing with Epoxy Groups . . . . . . . . . . . . 381<br />
10.4.3 Curing with Unsaturated Compounds . . . . . . 382<br />
10.4.4 Initiator Systems . . . . . . . . . . . . . . . . . 384<br />
10.5 Properties . . . . . . . . . . . . . . . . . . . . . . . . . 385<br />
10.5.1 Modelling . . . . . . . . . . . . . . . . . . . . 385<br />
10.6 <strong>Applications</strong> <strong>and</strong> Uses . . . . . . . . . . . . . . . . . . 385<br />
10.6.1 Composites . . . . . . . . . . . . . . . . . . . . 385<br />
10.6.2 Electronic Industry . . . . . . . . . . . . . . . . 385<br />
10.6.3 Spacecraft . . . . . . . . . . . . . . . . . . . . 386<br />
10.7 Special Formulations . . . . . . . . . . . . . . . . . . . 386<br />
10.7.1 PT Resins . . . . . . . . . . . . . . . . . . . . . 386<br />
10.7.2 Blends with Epoxies . . . . . . . . . . . . . . . 386<br />
10.7.3 Bismaleimide Triazine Resins . . . . . . . . . . 387<br />
10.7.4 Siloxane Crosslinked Resins . . . . . . . . . . . 388<br />
10.7.5 Alloys with Thermoplastics . . . . . . . . . . . 389<br />
10.7.6 Coupling Agents for Cyanate Ester Resins . . . 391<br />
References . . . . . . . . . . . . . . . . . . . . . . . . . . . . 391<br />
11 Bismaleimide Resins 397<br />
11.1 Monomers . . . . . . . . . . . . . . . . . . . . . . . . . 397<br />
11.1.1 4,4 ′ -Bis(maleimido)diphenylmethane . . . . . . 397<br />
11.1.2 2,2 ′ -Diallyl bisphenol A . . . . . . . . . . . . . 397<br />
11.1.3 Poly(ethylene glycol) End-capped with Maleimide 400
Contents<br />
xvii<br />
11.1.4 Bismaleimide Bisimides . . . . . . . . . . . . . 400<br />
11.1.5 Maleimide Epoxy Monomers . . . . . . . . . . 402<br />
11.1.6 Phosphorous-containing Monomers . . . . . . . 402<br />
11.1.7 Multiring Monomers with Pendant Chains . . . 405<br />
11.1.8 Reactions of Maleimides . . . . . . . . . . . . . 405<br />
11.1.9 Specialities . . . . . . . . . . . . . . . . . . . . 412<br />
11.2 Special Additives . . . . . . . . . . . . . . . . . . . . . 417<br />
11.2.1 Tougheners <strong>and</strong> Modifiers . . . . . . . . . . . . 417<br />
11.2.2 Fillers . . . . . . . . . . . . . . . . . . . . . . . 421<br />
11.2.3 Titanium dioxide . . . . . . . . . . . . . . . . . 421<br />
11.2.4 Reinforcing Materials . . . . . . . . . . . . . . 422<br />
11.2.5 Flame Retardants . . . . . . . . . . . . . . . . . 422<br />
11.3 Curing . . . . . . . . . . . . . . . . . . . . . . . . . . . 423<br />
11.3.1 Monitoring Curing Reactions . . . . . . . . . . 423<br />
11.3.2 Polymerization . . . . . . . . . . . . . . . . . . 423<br />
11.3.3 Interpenetrating Networks . . . . . . . . . . . . 429<br />
11.4 Properties . . . . . . . . . . . . . . . . . . . . . . . . . 431<br />
11.4.1 Thermal Properties . . . . . . . . . . . . . . . . 431<br />
11.4.2 Water Sorption . . . . . . . . . . . . . . . . . . 431<br />
11.4.3 Recycling . . . . . . . . . . . . . . . . . . . . . 433<br />
11.5 <strong>Applications</strong> <strong>and</strong> Uses . . . . . . . . . . . . . . . . . . 433<br />
11.5.1 Biochemical Reagents . . . . . . . . . . . . . . 433<br />
11.6 Special Formulations . . . . . . . . . . . . . . . . . . . 433<br />
11.6.1 Adhesives . . . . . . . . . . . . . . . . . . . . . 433<br />
11.6.2 Phosphazene-triazine <strong>Polymers</strong> . . . . . . . . . 435<br />
11.6.3 Phosphazene-triazine <strong>Polymers</strong> . . . . . . . . . 435<br />
11.6.4 Porous Networks . . . . . . . . . . . . . . . . . 435<br />
11.6.5 Nonlinear Optical Systems . . . . . . . . . . . . 435<br />
References . . . . . . . . . . . . . . . . . . . . . . . . . . . . 438<br />
12 Terpene Resins 447<br />
12.1 History . . . . . . . . . . . . . . . . . . . . . . . . . . 447<br />
12.2 Monomers . . . . . . . . . . . . . . . . . . . . . . . . . 447<br />
12.2.1 Resin . . . . . . . . . . . . . . . . . . . . . . . 448<br />
12.2.2 Turpentine . . . . . . . . . . . . . . . . . . . . 450<br />
12.2.3 Rosin . . . . . . . . . . . . . . . . . . . . . . . 450<br />
12.2.4 Production Data of Important Monomers . . . . 450<br />
12.3 Curing . . . . . . . . . . . . . . . . . . . . . . . . . . . 451
xviii<br />
<strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
12.3.1 Homopolymers . . . . . . . . . . . . . . . . . . 451<br />
12.3.2 Copolymers . . . . . . . . . . . . . . . . . . . . 452<br />
12.3.3 Terpene Phenolic Resins . . . . . . . . . . . . . 452<br />
12.3.4 Terpene Maleimide Resins . . . . . . . . . . . . 454<br />
12.4 Properties . . . . . . . . . . . . . . . . . . . . . . . . . 455<br />
12.4.1 Solubility . . . . . . . . . . . . . . . . . . . . . 455<br />
12.4.2 Adhesive Properties . . . . . . . . . . . . . . . 456<br />
12.4.3 Characterization . . . . . . . . . . . . . . . . . 458<br />
12.4.4 Recycling . . . . . . . . . . . . . . . . . . . . . 459<br />
12.5 <strong>Applications</strong> <strong>and</strong> Uses . . . . . . . . . . . . . . . . . . 459<br />
12.5.1 Sealants . . . . . . . . . . . . . . . . . . . . . . 460<br />
12.5.2 Pressure-sensitive Adhesives . . . . . . . . . . . 460<br />
12.5.3 Polyacrylate Hot-melt Pressure-sensitive Adhesives 461<br />
12.5.4 Hot-Melt Adhesives . . . . . . . . . . . . . . . 462<br />
12.5.5 Coatings . . . . . . . . . . . . . . . . . . . . . 463<br />
12.5.6 Sizing Agents . . . . . . . . . . . . . . . . . . . 463<br />
12.5.7 Toner Compositions . . . . . . . . . . . . . . . 465<br />
12.5.8 Chewing Gums . . . . . . . . . . . . . . . . . . 465<br />
12.6 Special Formulations . . . . . . . . . . . . . . . . . . . 466<br />
12.6.1 Toughener for Novolaks . . . . . . . . . . . . . 466<br />
12.6.2 Fluoro Copolymers . . . . . . . . . . . . . . . . 467<br />
References . . . . . . . . . . . . . . . . . . . . . . . . . . . . 467<br />
13 Cyanoacrylates 471<br />
13.1 Monomers . . . . . . . . . . . . . . . . . . . . . . . . . 471<br />
13.1.1 Synthesis . . . . . . . . . . . . . . . . . . . . . 471<br />
13.1.2 Crosslinkers . . . . . . . . . . . . . . . . . . . 472<br />
13.1.3 Commercial Products . . . . . . . . . . . . . . 473<br />
13.2 Special Additives . . . . . . . . . . . . . . . . . . . . . 475<br />
13.2.1 Plasticizers . . . . . . . . . . . . . . . . . . . . 475<br />
13.2.2 Accelerators . . . . . . . . . . . . . . . . . . . 477<br />
13.2.3 Thickeners . . . . . . . . . . . . . . . . . . . . 480<br />
13.2.4 Stabilizers . . . . . . . . . . . . . . . . . . . . 480<br />
13.2.5 Primers . . . . . . . . . . . . . . . . . . . . . . 482<br />
13.2.6 Diazabicyclo <strong>and</strong> Triazabicyclo Primers . . . . . 483<br />
13.2.7 Polyamine Dendrimers . . . . . . . . . . . . . . 484<br />
13.3 Curing . . . . . . . . . . . . . . . . . . . . . . . . . . . 485<br />
13.3.1 Photo Curing . . . . . . . . . . . . . . . . . . . 485
Contents<br />
xix<br />
13.4 Properties . . . . . . . . . . . . . . . . . . . . . . . . . 486<br />
13.5 <strong>Applications</strong> <strong>and</strong> Uses . . . . . . . . . . . . . . . . . . 486<br />
13.5.1 Manicure Composition . . . . . . . . . . . . . . 486<br />
13.5.2 Tissue Adhesives . . . . . . . . . . . . . . . . . 487<br />
References . . . . . . . . . . . . . . . . . . . . . . . . . . . . 489<br />
14 Benzocyclobutene Resins 493<br />
14.1 Modified <strong>Polymers</strong> . . . . . . . . . . . . . . . . . . . . 498<br />
14.1.1 Thermotropic Copolymers . . . . . . . . . . . . 498<br />
14.1.2 BCB-modified Aromatic Polyamides . . . . . . 498<br />
14.1.3 BCB End-capped Polyimides . . . . . . . . . . 498<br />
14.1.4 Flame Resistant Formulations . . . . . . . . . . 501<br />
14.2 Crosslinkers . . . . . . . . . . . . . . . . . . . . . . . . 501<br />
14.2.1 Modified Poly(ethylene terephthalate) . . . . . . 501<br />
14.3 <strong>Applications</strong> <strong>and</strong> Uses . . . . . . . . . . . . . . . . . . 501<br />
14.3.1 <strong>Applications</strong> in Microelectronics . . . . . . . . 502<br />
14.3.2 Optical <strong>Applications</strong> . . . . . . . . . . . . . . . 504<br />
References . . . . . . . . . . . . . . . . . . . . . . . . . . . . 504<br />
15 <strong>Reactive</strong> Extrusion 507<br />
15.1 Extruder . . . . . . . . . . . . . . . . . . . . . . . . . . 508<br />
15.1.1 Heat of Polymerization . . . . . . . . . . . . . . 510<br />
15.1.2 Ceiling Temperature . . . . . . . . . . . . . . . 510<br />
15.1.3 Strategy of <strong>Reactive</strong> Extrusion . . . . . . . . . . 511<br />
15.2 Compositions of Industrial <strong>Polymers</strong> . . . . . . . . . . . 512<br />
15.2.1 Poly(styrene) . . . . . . . . . . . . . . . . . . . 513<br />
15.2.2 Poly(tetramethylene ether) <strong>and</strong> Poly(caprolactam) 513<br />
15.2.3 Polyamide 12 . . . . . . . . . . . . . . . . . . . 513<br />
15.2.4 Poly(butyl methacrylate) . . . . . . . . . . . . . 514<br />
15.2.5 Poly(carbonate) . . . . . . . . . . . . . . . . . . 514<br />
15.3 Biodegradable Compositions . . . . . . . . . . . . . . . 517<br />
15.3.1 Poly(lactide)s . . . . . . . . . . . . . . . . . . . 519<br />
15.3.2 Biodegradable Fibers . . . . . . . . . . . . . . . 521<br />
15.3.3 Poly(ε-caprolactone) . . . . . . . . . . . . . . . 521<br />
15.3.4 Cationically Modified Starch . . . . . . . . . . . 523<br />
15.3.5 Blends of Starch <strong>and</strong> Poly(acrylamide) . . . . . 523<br />
15.3.6 Blends of Protein <strong>and</strong> Polyester . . . . . . . . . 523<br />
15.4 Chain Extenders . . . . . . . . . . . . . . . . . . . . . . 524<br />
15.4.1 Recycling of Poly(ethylene-terephthalate) . . . . 524
xx<br />
<strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
15.4.2 Modified Poly(ethylene terephthalate) . . . . . . 524<br />
15.4.3 Poly(butylene terephthalate) . . . . . . . . . . . 525<br />
15.5 Related <strong>Applications</strong> . . . . . . . . . . . . . . . . . . . 525<br />
15.5.1 Transesterification . . . . . . . . . . . . . . . . 525<br />
15.5.2 Hydrolysis <strong>and</strong> Alcoholysis . . . . . . . . . . . 526<br />
15.5.3 Flame Retardant Master Batch . . . . . . . . . . 526<br />
References . . . . . . . . . . . . . . . . . . . . . . . . . . . . 526<br />
16 Compatibilization 531<br />
16.1 Equipment . . . . . . . . . . . . . . . . . . . . . . . . . 532<br />
16.2 Basic Terms . . . . . . . . . . . . . . . . . . . . . . . . 532<br />
16.2.1 Thermodynamic Compatibility . . . . . . . . . 532<br />
16.2.2 Thermodynamic Models . . . . . . . . . . . . . 533<br />
16.2.3 Particle Size . . . . . . . . . . . . . . . . . . . 533<br />
16.2.4 Interfacial Slip . . . . . . . . . . . . . . . . . . 534<br />
16.2.5 Interpolymer Radical Coupling . . . . . . . . . 534<br />
16.2.6 Technological Compatibility . . . . . . . . . . . 534<br />
16.3 Compatibilization by Additives . . . . . . . . . . . . . . 538<br />
16.3.1 Poly(ethylene) Blended with Inorganic Fillers . . 538<br />
16.3.2 Filler Materials without Chemical Compatibilizers 538<br />
16.3.3 Modified Inorganic Fillers . . . . . . . . . . . . 539<br />
16.3.4 Clay Nanocomposites . . . . . . . . . . . . . . 540<br />
16.3.5 Thermoplastic Elastomers . . . . . . . . . . . . 540<br />
16.3.6 Polyamide 6,6 <strong>and</strong> Poly(butylene terephthalate) . 541<br />
16.3.7 Poly(ethylene)/Wood Flour Composites . . . . . 541<br />
16.3.8 Recycled Polyolefins . . . . . . . . . . . . . . . 542<br />
16.3.9 Block Copolymers . . . . . . . . . . . . . . . . 542<br />
16.3.10 Impact Modification of Waste PET . . . . . . . 544<br />
16.3.11 Starch . . . . . . . . . . . . . . . . . . . . . . . 544<br />
16.3.12 Blends of Cellulose <strong>and</strong> Chitosan . . . . . . . . 545<br />
16.4 <strong>Reactive</strong> Compatibilization . . . . . . . . . . . . . . . . 545<br />
16.4.1 Coupling Agents for Compatibilization . . . . . 548<br />
16.4.2 Vector Fluids . . . . . . . . . . . . . . . . . . . 549<br />
16.4.3 Poly(ethylene) <strong>and</strong> Polyamide 6 . . . . . . . . . 549<br />
16.4.4 PEO <strong>and</strong> PBT . . . . . . . . . . . . . . . . . . 551<br />
16.4.5 Poly(ethylene-octene) <strong>and</strong> Polyamide 6 . . . . . 552<br />
16.4.6 Ethylene Acrylic Acid Copolymers <strong>and</strong> Polyamide<br />
6 . . . . . . . . . . . . . . . . . . . . . . . 552
Contents<br />
xxi<br />
16.4.7 Sisal Fibers . . . . . . . . . . . . . . . . . . . . 552<br />
16.4.8 Thermotropic Liquid Crystalline Polyesters . . . 553<br />
16.4.9 Ionomers <strong>and</strong> Ionomeric Compatibilizers . . . . 554<br />
16.4.10 Poly(styrene) . . . . . . . . . . . . . . . . . . . 556<br />
16.4.11 Polyolefins/Poly(ethylene oxide) . . . . . . . . . 558<br />
16.4.12 Poly(phenylene sulfide)/Liquid Crystalline <strong>Polymers</strong><br />
. . . . . . . . . . . . . . . . . . . . . . . 559<br />
16.4.13 LDPE/Thermoplastic Starch . . . . . . . . . . . 559<br />
16.4.14 PE <strong>and</strong> EVA . . . . . . . . . . . . . . . . . . . 559<br />
16.4.15 SBR <strong>and</strong> EVA . . . . . . . . . . . . . . . . . . 560<br />
16.4.16 NBR <strong>and</strong> EPDM . . . . . . . . . . . . . . . . . 560<br />
16.4.17 NBR <strong>and</strong> PA6 . . . . . . . . . . . . . . . . . . 561<br />
16.4.18 Poly(carbonate)–Poly(vinylidene fluoride) Blends 561<br />
16.4.19 Bisphenol A-poly(carbonate) <strong>and</strong> ABS Copolymers 561<br />
16.4.20 Kevlar . . . . . . . . . . . . . . . . . . . . . 563<br />
16.4.21 Polyamides . . . . . . . . . . . . . . . . . . . . 563<br />
16.4.22 Polyethers . . . . . . . . . . . . . . . . . . . . 564<br />
16.4.23 Polyurethane <strong>and</strong> Poly(ethylene terephthalate) . 566<br />
16.5 Functionalization of End Groups . . . . . . . . . . . . . 566<br />
16.5.1 Mechanisms . . . . . . . . . . . . . . . . . . . 566<br />
16.5.2 Amino-terminated Nitrile Rubber . . . . . . . . 569<br />
16.5.3 Functionalization of Olefinic End Groups of Poly-<br />
(propylene) . . . . . . . . . . . . . . . . . . . . 569<br />
16.5.4 Muconic Acid Grafted Polyolefin Compatibilizers 573<br />
16.5.5 Polyfunctional <strong>Polymers</strong> <strong>and</strong> Modified Polyolefin 573<br />
References . . . . . . . . . . . . . . . . . . . . . . . . . . . . 574<br />
17 Rheology Control 587<br />
17.1 Melt Flow Rate . . . . . . . . . . . . . . . . . . . . . . 587<br />
17.2 Rheology Control Techniques . . . . . . . . . . . . . . 587<br />
17.2.1 Pelletizing . . . . . . . . . . . . . . . . . . . . 589<br />
17.3 Peroxides for Rheology Control . . . . . . . . . . . . . 590<br />
17.3.1 Hydroperoxides . . . . . . . . . . . . . . . . . 590<br />
17.3.2 Peroxides . . . . . . . . . . . . . . . . . . . . . 591<br />
17.3.3 Diacyl Peroxides . . . . . . . . . . . . . . . . . 593<br />
17.3.4 Ketone Peroxides . . . . . . . . . . . . . . . . . 593<br />
17.3.5 Masterbatches of Peroxides . . . . . . . . . . . 595<br />
17.3.6 Peresters . . . . . . . . . . . . . . . . . . . . . 595
xxii<br />
<strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
17.3.7 Properties of Peroxides . . . . . . . . . . . . . . 595<br />
17.3.8 Azo Compounds . . . . . . . . . . . . . . . . . 600<br />
17.4 Scavengers . . . . . . . . . . . . . . . . . . . . . . . . 601<br />
17.4.1 Stable Nitroxyl Radicals . . . . . . . . . . . . . 601<br />
17.5 Mechanism of Degradation . . . . . . . . . . . . . . . . 601<br />
17.6 Ultra High Melt Flow Poly(propylene) . . . . . . . . . . 605<br />
17.7 Irregular Flow Improvement . . . . . . . . . . . . . . . 605<br />
17.8 Heterophasic Copolymers . . . . . . . . . . . . . . . . . 606<br />
17.9 Poly(propylene) . . . . . . . . . . . . . . . . . . . . . . 608<br />
17.9.1 Long Chain Branched Poly(propylene) . . . . . 608<br />
17.9.2 Effect of MFR on Temperature <strong>and</strong> Residence Time 608<br />
References . . . . . . . . . . . . . . . . . . . . . . . . . . . . 609<br />
18 Grafting 611<br />
18.1 The Techniques in Grafting . . . . . . . . . . . . . . . . 611<br />
18.1.1 Parameters that Influence Grafting . . . . . . . . 611<br />
18.1.2 Free Radical Induced Grafting . . . . . . . . . . 614<br />
18.1.3 Grafting Using Stable Radicals . . . . . . . . . 614<br />
18.2 Polyolefins . . . . . . . . . . . . . . . . . . . . . . . . 616<br />
18.2.1 Monomers for Grafting onto Polyolefins . . . . 616<br />
18.2.2 Mechanism of Melt Grafting . . . . . . . . . . . 617<br />
18.2.3 Side Reactions . . . . . . . . . . . . . . . . . . 618<br />
18.2.4 Viscosity . . . . . . . . . . . . . . . . . . . . . 618<br />
18.2.5 Ceiling Temperature . . . . . . . . . . . . . . . 620<br />
18.2.6 Effect of Initiator Solubility . . . . . . . . . . . 620<br />
18.2.7 Distribution of the Grafted Groups . . . . . . . . 622<br />
18.2.8 Effect of Stabilizers on Grafting . . . . . . . . . 622<br />
18.2.9 Radical Grafting of Polyolefins with Diethyl<br />
Maleate . . . . . . . . . . . . . . . . . . . . . . 622<br />
18.2.10 Inhibitors for the Homopolymerization of Maleic<br />
anhydride . . . . . . . . . . . . . . . . . . . . . 623<br />
18.2.11 Inhibitors for Crosslinking . . . . . . . . . . . . 623<br />
18.2.12 Special Initiators . . . . . . . . . . . . . . . . . 624<br />
18.2.13 Maleic anhydride . . . . . . . . . . . . . . . . . 629<br />
18.2.14 Polyolefins Grafted with Itaconic Acid Derivatives 629<br />
18.2.15 Imidized Maleic Groups . . . . . . . . . . . . . 630<br />
18.2.16 Oxazoline-modified Polyolefins . . . . . . . . . 630<br />
18.2.17 Modification of Polyolefins with Vinylsilanes . . 631
Contents<br />
xxiii<br />
18.2.18 Ethyl Diazoacetate-modified Polyolefins . . . . 631<br />
18.2.19 Grafting Antioxidants . . . . . . . . . . . . . . 632<br />
18.2.20 Comonomer Assisted Free Radical Grafting . . . 633<br />
18.2.21 Radiation Induced Grafting in Solution . . . . . 636<br />
18.2.22 Characterization of Polyolefin Graft Copolymers 636<br />
18.2.23 PVC/LDPE Melt Blends . . . . . . . . . . . . . 637<br />
18.3 Other <strong>Polymers</strong> . . . . . . . . . . . . . . . . . . . . . . 637<br />
18.3.1 Poly(styrene) Functionalized with Maleic anhydride<br />
. . . . . . . . . . . . . . . . . . . . . . . 637<br />
18.3.2 Multifunctional Monomers for PP/PS Blends . . 637<br />
18.3.3 Poly(ethylene-co-methyl acrylate) . . . . . . . . 638<br />
18.3.4 n-Butyl methacrylate Grafted onto PVC . . . . . 638<br />
18.3.5 Starch Esterification . . . . . . . . . . . . . . . 639<br />
18.3.6 Starch Grafted Acrylics . . . . . . . . . . . . . 639<br />
18.3.7 Thermoplastic Phenol/Formaldehyde <strong>Polymers</strong> . 640<br />
18.3.8 Polyesters <strong>and</strong> Polyurethanes . . . . . . . . . . 640<br />
18.3.9 Polyacrylic Hot-melt Pressure-sensitive Adhesive 642<br />
18.4 Terminal Functionalization . . . . . . . . . . . . . . . . 642<br />
18.4.1 Ene Reaction with Poly(propylene) . . . . . . . 642<br />
18.4.2 Styrene-butadiene Rubber . . . . . . . . . . . . 643<br />
18.4.3 Diels-Alder Reaction . . . . . . . . . . . . . . . 643<br />
18.5 Grafting onto Surfaces . . . . . . . . . . . . . . . . . . 644<br />
18.5.1 Grafting onto Poly(ethylene) . . . . . . . . . . . 644<br />
18.5.2 Grafting onto Poly(tetrafluoroethylene) . . . . . 647<br />
References . . . . . . . . . . . . . . . . . . . . . . . . . . . . 649<br />
19 Acrylic Dental Fillers 657<br />
19.1 History . . . . . . . . . . . . . . . . . . . . . . . . . . 658<br />
19.2 Polymeric Composite Filling Materials . . . . . . . . . . 658<br />
19.3 Monomers . . . . . . . . . . . . . . . . . . . . . . . . . 659<br />
19.3.1 Acrylics <strong>and</strong> Methacrylics . . . . . . . . . . . . 659<br />
19.3.2 Cyclic Monomers . . . . . . . . . . . . . . . . 665<br />
19.3.3 Epoxy Monomers . . . . . . . . . . . . . . . . 666<br />
19.3.4 Highly Loaded Composite . . . . . . . . . . . . 668<br />
19.4 Radical Polymerization . . . . . . . . . . . . . . . . . . 668<br />
19.4.1 Chemical Curing Systems . . . . . . . . . . . . 668<br />
19.4.2 Photo Curing . . . . . . . . . . . . . . . . . . . 673<br />
19.4.3 Curing Techniques . . . . . . . . . . . . . . . . 676
xxiv<br />
<strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
19.4.4 Dual Initiator Systems . . . . . . . . . . . . . . 676<br />
19.5 Inhibitors . . . . . . . . . . . . . . . . . . . . . . . . . 677<br />
19.6 Additives . . . . . . . . . . . . . . . . . . . . . . . . . 677<br />
19.6.1 Fillers <strong>and</strong> Reinforcing Materials . . . . . . . . 677<br />
19.6.2 Pigments . . . . . . . . . . . . . . . . . . . . . 681<br />
19.6.3 Photostabilizers . . . . . . . . . . . . . . . . . . 681<br />
19.6.4 Caries Inhibiting Agents . . . . . . . . . . . . . 682<br />
19.6.5 Coloring or Tint Agents . . . . . . . . . . . . . 682<br />
19.6.6 Adhesion Promoter . . . . . . . . . . . . . . . . 682<br />
19.6.7 Thermochromic Dye . . . . . . . . . . . . . . . 686<br />
19.7 Properties . . . . . . . . . . . . . . . . . . . . . . . . . 686<br />
19.7.1 Water Sorption . . . . . . . . . . . . . . . . . . 686<br />
19.7.2 Cytotoxicity . . . . . . . . . . . . . . . . . . . 687<br />
19.8 <strong>Applications</strong> . . . . . . . . . . . . . . . . . . . . . . . . 687<br />
19.8.1 Filling Techniques . . . . . . . . . . . . . . . . 687<br />
19.8.2 Primer Emulsions . . . . . . . . . . . . . . . . 688<br />
References . . . . . . . . . . . . . . . . . . . . . . . . . . . . 688<br />
20 Toners 693<br />
20.1 Toner Components . . . . . . . . . . . . . . . . . . . . 694<br />
20.2 Toner Resins . . . . . . . . . . . . . . . . . . . . . . . 695<br />
20.3 Manufacture of Toner Resins . . . . . . . . . . . . . . . 696<br />
20.3.1 Suspension Polymerization . . . . . . . . . . . 696<br />
20.3.2 Terephthalic Ester Resins . . . . . . . . . . . . 697<br />
20.3.3 Unsaturated Ester Resins . . . . . . . . . . . . . 697<br />
20.3.4 Toner Resins with Low Fix Temperature . . . . 698<br />
20.3.5 Toners for Textile Printing . . . . . . . . . . . . 700<br />
20.4 Characterization of Toners . . . . . . . . . . . . . . . . 701<br />
References . . . . . . . . . . . . . . . . . . . . . . . . . . . . 701<br />
Index 703<br />
Acronyms . . . . . . . . . . . . . . . . . . . . . . . . . . . . 703<br />
Chemicals . . . . . . . . . . . . . . . . . . . . . . . . . . . . 724<br />
General . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 757
1<br />
Unsaturated Polyester Resins<br />
Unsaturated polyester resins consist of two polymers, i.e., a short chain<br />
polyester containing polymerizable double bonds <strong>and</strong> a vinyl monomer.<br />
The curing reaction consists of a copolymerization of the vinyl monomer<br />
with the double bonds of the polyester. In the course of curing, a three-dimensional<br />
network is formed. Unsaturated polyester resins belong to the<br />
group of so-called thermosets. There are several monographs <strong>and</strong> reviews<br />
on unsaturated polyesters <strong>and</strong> unsaturated polyester resins. 1–7<br />
We will differentiate between unsaturated polyesters <strong>and</strong> unsaturated<br />
polyester resins. Unsaturated polyesters are the polyesters as they<br />
emerge from the condensation vessel. They are rarely sold as such, because<br />
they are brittle at room temperature <strong>and</strong> difficult to h<strong>and</strong>le. Instead,<br />
whenever a polyester is freshly synthesized in a plant, it is mixed with the<br />
vinyl monomer in the molten state. Thus materials that are viscous at room<br />
temperature, with a styrene content of ca. 60% are sold. Such a mixture<br />
of an unsaturated polyester with the vinyl polymer is referred to here as an<br />
unsaturated polyester resin.<br />
1.1 HISTORY<br />
It was realized long ago that some natural oils as well as alkyde resins can<br />
be dried by certain additives <strong>and</strong> used as coatings. This drying results from<br />
a polymerization of the unsaturated moieties in the ester molecules. Next<br />
it was discovered that the addition of styrene would accelerate the drying.<br />
1
2 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
CH 3<br />
HO<br />
CH 2 CH 2<br />
OH<br />
HO<br />
CH CH 2<br />
OH<br />
Ethylene glycol<br />
Propylene glycol<br />
CH 3<br />
HO<br />
CH 2<br />
C CH 2<br />
CH 3<br />
OH<br />
Neopentyl glycol<br />
H 3 C<br />
CH 2 OH<br />
CH 2 C CH 2 OH<br />
CH 2 OH<br />
CH 2 CH CH 2<br />
OH<br />
OH OH<br />
Trimethylol propane<br />
Glycerol<br />
Figure 1.1: Diols <strong>and</strong> Triols Used for Unsaturated Polyester Resins<br />
The invention of unsaturated polyester resins is ascribed to Carleton Ellis<br />
(1876–1941). The first patents with regard to polyester resins emerged in<br />
the 1930’s. 8–10 Commercial production started in 1941 already reinforced<br />
with glass fibers for radar domes, also referred to as radomes.<br />
1.2 MONOMERS<br />
According to the composition of an unsaturated polyester resin, the monomers<br />
can be grouped in two main classes, i.e., components for the polyester<br />
<strong>and</strong> components for the vinyl monomer.<br />
1.2.1 Monomers for the Unsaturated Polyester (UP)<br />
Monomers used for unsaturated polyesters are shown in Table 1.1 <strong>and</strong> in<br />
Figures 1.1 <strong>and</strong> 1.2. Unsaturated diols are only rarely used.
Unsaturated Polyester Resins 3<br />
Saturated alcohols<br />
1,2-Propylene glycol<br />
Ethylene glycol<br />
Diethylene glycol<br />
Neopentyl glycol<br />
Glycerol<br />
Table 1.1: Monomers for Unsaturated Polyesters<br />
Tetrabromobisphenol A (TBBPA)<br />
Trimethylolpropane<br />
Trimethylolpropane mono allyl ether<br />
(TMPAE)<br />
Undecanol<br />
Saturated acids <strong>and</strong> anhydrides<br />
Remarks<br />
Most common glycol<br />
Less compatible with styrene than<br />
Propylene glycol<br />
Good drying properties<br />
Good hydrolysis resistance<br />
Trifunctional alcohol, for branched<br />
polyesters. Danger of crosslinking<br />
during condensation<br />
Flame retardant<br />
Trifunctional alcohol, cheaper than<br />
glycerol<br />
Weather resistant for coatings11, 12<br />
Used as chain stopper<br />
Remarks<br />
Phthalic anhydride<br />
Most common anhydride<br />
Isophthalic acid<br />
Good hydrolysis resistance<br />
Terephthalic acid<br />
Superior hydrolysis resistance<br />
HET acid<br />
Flame retardant systems. In fact, even<br />
when addressed as HET acid, the<br />
HET anhydride is used<br />
Tetrabromophthalic anhydride Flame retardant systems<br />
Adipic acid<br />
Soft resins<br />
Sebacic acid<br />
Soft resins<br />
o-Carboxy phthalanilic acid<br />
13<br />
Unsaturated acids <strong>and</strong> anhydrides<br />
Maleic anhydride<br />
Fumaric acid<br />
Itaconic acid<br />
Remarks<br />
Most common<br />
Copolymerizes better with styrene<br />
than maleic anhydride
4 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
COOH<br />
O<br />
O<br />
Phthalic anhydride<br />
COOH<br />
Isophthalic acid<br />
COOH<br />
Cl<br />
Cl<br />
Cl<br />
Cl<br />
O<br />
Cl<br />
Cl<br />
O<br />
COOH<br />
Terephthalic acid<br />
O<br />
HET-anhydride<br />
H<br />
O<br />
H<br />
O<br />
O<br />
CH<br />
HOOC<br />
COOH<br />
CH<br />
Maleic anhydride<br />
Fumaric acid<br />
Figure 1.2: Acids <strong>and</strong> Anhydrides Used for Unsaturated Polyester Resins
Unsaturated Polyester Resins 5<br />
1.2.1.1 Alcohol Components<br />
The most common alcohol components are 1,2-propylene glycol <strong>and</strong> ethylene<br />
glycol. Ether containing alcohols exhibit better air drying properties<br />
<strong>and</strong> are used in topcoats. Polyesters based on unsaturated diols can be prepared<br />
by the transesterification of diethyl adipate with unsaturated diols,<br />
e.g., cis-2-butene-1,4-diol, <strong>and</strong> 2-butyne-1,4-diol. The transesterification<br />
method is a suitable procedure for the preparation of unsaturated polyesters<br />
in comparison to the direct polycondensation. 14 cis-2-Butene-1,4-diol, the<br />
most available aliphatic unsaturated diol, has been used to produce some<br />
valuable polymers such as graftable unsaturated segmented polyurethanes<br />
<strong>and</strong> crosslinkable polyesters for medical purposes.<br />
1.2.1.2 Acid <strong>and</strong> Anhydride Components<br />
A general purpose industrial unsaturated polyester is made from 1,2-propylene<br />
glycol, phthalic anhydride, <strong>and</strong> maleic anhydride. The most commonly<br />
used vinyl monomer is styrene. Maleic anhydride without phthalic<br />
anhydride would yield a polyester with a high density of double bonds<br />
along the polyester chain. This would result in a high crosslinking density<br />
of the cured product, thus in a brittle product. Therefore, the unsaturated<br />
acid component is always diluted with an acid with non-polymerizable<br />
double bonds. Note that aromatic double bonds also will not polymerize<br />
with vinyl components. The double bond in HET acid will not polymerize.<br />
Fumaric acid copolymerizes well with styrene, but fumaric acid is more<br />
costly than maleic anhydride. Therefore, maleic anhydride is the preferred<br />
unsaturated acid component. Another aspect is that during the condensation<br />
of fumaric acid, 2 mol of water must be removed from the reaction<br />
mixtures, whereas in the case of maleic anhydride only 1 mol of water<br />
must be removed. Anhydrides are preferred over the corresponding acids<br />
because of the higher reactivity.<br />
Isophthalic acid <strong>and</strong> terephthalic acid cannot form an anhydride.<br />
These compounds do not condense as fast as phthalic anhydride. On the<br />
other h<strong>and</strong>, the polyesters from isophthalic acid <strong>and</strong> terephthalic acid are<br />
more stable than those made from phthalic anhydride. That is why these<br />
polyesters with neopentyl glycol are used in aggressive environments <strong>and</strong><br />
also as gel coats <strong>and</strong> top coats. A gel coat is the first layer of a multi layer<br />
material; the top coat is the layer on the opposite side. For instance, if a<br />
polyester boat is built, the gel coat is first painted into the model. Then
6 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
a series of glass fiber reinforced laminates are applied, <strong>and</strong> finally the top<br />
coat is painted.<br />
Isomerization. During the synthesis of the polyester, maleic anhydride<br />
partly isomerizes to fumaric acid. The isomerization follows a secondorder<br />
kinetics because of the catalysis by maleic acid. The activation energy<br />
of the isomerization is ca. 63.2 kJ/mol. 15<br />
2-Methyl-1,3-propanediol offers significant process advantages to<br />
resin producers because it is an easily h<strong>and</strong>led liquid, it has a high boiling<br />
point, <strong>and</strong> it has two primary hydroxyl groups for rapid condensations.<br />
Polyester resins produced from 2-methyl-1,3-propanediol using conventional<br />
condensation polymerization, however, have relatively low fumarate<br />
contents (60 to 70%), <strong>and</strong> simply increasing the reaction temperature to<br />
promote isomerization causes color problems.<br />
The two-step process helps increase the degree of isomerization for<br />
such systems. First, the aromatic dicarboxylic acid is allowed to react with<br />
2-methyl-1,3-propanediol at a temperature of up to 225°C to produce an<br />
ester diol intermediate. In the second step, the intermediate reacts with<br />
maleic anhydride <strong>and</strong> with 1,2-propylene glycol. The resulting unsaturated<br />
polyester resin has a fumarate content greater than about 85%. 16 The high<br />
fumarate content helps the resins to cure quickly <strong>and</strong> thoroughly with vinyl<br />
monomers, giving the resulting thermosets excellent water resistance.<br />
1.2.1.3 Amine Modifiers<br />
The adducts of ethylene oxide or propylene oxide with N,N ′ -diphenylethane-1,2-diamine<br />
or N,N-dimethyl-p-phenylene diamine <strong>and</strong> ethylene oxide<br />
with N,N ′ -diphenylhexane-1,6-diamine can be used as modifiers. When<br />
used in amounts up to 2%, the amines substantially reduce the gelation<br />
time of these modified unsaturated polyesters. However, as the reactivity<br />
of the resins increases, their stability decreases.<br />
17, 18<br />
1.2.1.4 Dicyclopentadiene<br />
Dicyclopentadiene is used in a wide variety of applications, including elastomers,<br />
flame retardants, pesticides, <strong>and</strong> resins for adhesives, coatings <strong>and</strong><br />
rubber tackifiers. Approximately 30% of the production is used for unsaturated<br />
polyester resins because of its valuable properties. 19
Unsaturated Polyester Resins 7<br />
O<br />
O<br />
OH<br />
OH<br />
+<br />
O<br />
O<br />
OH<br />
H<br />
O<br />
Figure 1.3: Ene Reaction between Maleic acid <strong>and</strong> Dicyclopentadiene<br />
O<br />
O<br />
O<br />
O<br />
+<br />
O<br />
O<br />
O<br />
O<br />
Figure 1.4: Retro Diels-Alder Reaction of Dicyclopentadiene <strong>and</strong> Diels-Alder<br />
Reaction between Maleic acid units <strong>and</strong> Cyclopentadiene<br />
Dicyclopentadiene polyester resins are synthesized from dicyclopentadiene,<br />
maleic anhydride, <strong>and</strong> a glycol. The reaction is performed<br />
in the presence of water to generate maleic acid from the maleic anhydride<br />
to form dicyclopentadiene maleate. The ene reaction is shown in<br />
Figure 1.3.<br />
The maleate is esterified with the glycol to form the unsaturated<br />
polyester resin. 20, 21 The ene adduct serves to form end-capped polyesters.<br />
At higher temperatures dicyclopentadiene undergoes a retro Diels-Alder<br />
reaction <strong>and</strong> can add to the unsaturations of fumaric acid <strong>and</strong> maleic acid<br />
(as pointed out in Figure 1.4), to form nadic acid units When the dicyclopentadiene-modified<br />
unsaturated polyester is used for a molding material,<br />
the polyester is usually mixed with a radically polymerizable monomer <strong>and</strong><br />
a polymerization initiator. This allows the viscosity or curing time of the<br />
molding material to be suitable for the molding operation.
8 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Monomer<br />
Table 1.2: Vinyl Monomers for Unsaturated Polyester Resins<br />
Styrene<br />
p-Vinyltoluene<br />
α-Methylstyrene<br />
Methyl acrylate<br />
Methyl methacrylate<br />
Diallyl phthalate<br />
Triallyl cyanurate<br />
Remarks<br />
Most common, but carcinogenic<br />
Not really a substitute for styrene<br />
Slower curing reaction to avoid thermal stress<br />
Good optical properties<br />
Dicyclopentadiene-modified unsaturated polyesters yield molded articles<br />
with excellent performance. The function of dicyclopentadiene is to<br />
impart air drying characteristics, low-profile properties, high heat distortion,<br />
excellent weathering performance, <strong>and</strong> increased filler dispersibility<br />
in the resulting polymer. 22<br />
1.2.2 Vinyl Monomers<br />
The vinyl monomer serves as solvent for the polyester <strong>and</strong> reduces its viscosity.<br />
Further, it is the agent of copolymerization in the course of curing.<br />
Vinyl monomers for unsaturated polyester resins are shown in Table 1.2<br />
<strong>and</strong> in Figure 1.5.<br />
1.2.2.1 Styrenes<br />
Styrene is the most widely used vinyl monomer for unsaturated polyesters.<br />
However, styrene has a carcinogenic potential: therefore,replacing styrene<br />
by some other vinyl monomer has been discussed for years.<br />
With larger amounts of styrene the rigidity of the material can be<br />
increased. α-Methylstyrene forms less reactive radicals, <strong>and</strong> thus slows<br />
down the curing reaction. Therefore, α-methylstyrene is suitable for decreasing<br />
the peak temperature during curing.<br />
Polar vinyl monomers, such as vinylpyridine, improve the adhesion<br />
of the polyester to glass fibers, which is useful in preventing delamination.<br />
1.2.2.2 Acrylates <strong>and</strong> Methacrylates<br />
Acrylates improve outdoor stability. Methyl methacrylate, in particular,<br />
enhances the optical properties. The refractive index can be varied with
Unsaturated Polyester Resins 9<br />
CH CH 2<br />
CH CH 2<br />
CH 3<br />
Styrene<br />
p-Vinyltoluene<br />
CH 3<br />
C CH 2<br />
CH 2<br />
C<br />
O<br />
O<br />
CH 2 CH 2<br />
CH 3<br />
α-Methylstyrene<br />
Methyl methacrylate<br />
O<br />
C<br />
C<br />
O<br />
O<br />
CH 2<br />
CH<br />
CH 2<br />
CH<br />
CH 2<br />
CH 2<br />
O<br />
Diallyl phthalate<br />
Figure 1.5: Vinyl Monomers for Unsaturated Polyester Resins
10 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
CH 2 CH 2 O CH 2 CH 2 O CH 2 CH 2<br />
O<br />
CH<br />
O<br />
CH<br />
CH 2 CH 2<br />
Triethylene glycol divinyl ether<br />
Figure 1.6: Vinyl ethers<br />
mixtures of styrene <strong>and</strong> methyl methacrylate close to that of glass, so that<br />
fairly transparent materials could be produced.<br />
1.2.2.3 Vinyl Ethers<br />
Various vinyl <strong>and</strong> divinyl ethers have been used as substitutes for styrene.<br />
Divinyl ethers with unsaturated polyesters are used preferably in radiation<br />
curable compositions <strong>and</strong> coatings. However, special formulations containing<br />
no styrene but triethylene glycol divinyl ether (c.f. Figure 1.6) are<br />
available that can be used for gel coats. 23<br />
Propenyl ethers are generally easier to prepare than their corresponding<br />
vinyl ethers. The propenyl ethers are simply prepared by isomerization<br />
of the corresponding allyl ethers. Due to the steric effect of the methyl<br />
groups in the propenyl ether molecules, they are expected to be much less<br />
reactive than their vinyl ether analogs. 24 Examples for propenyl ethers are<br />
ethoxylated hexanediol dipropenyl ether <strong>and</strong>, 1,1,1-trimethylolpropane dipropenyl<br />
ether.<br />
1.2.2.4 Other Vinyl Monomers<br />
Triallyl cyanurate enhances the thermal stability of the final products. Since<br />
the compound is trifunctional, it enhances the crosslinking density.<br />
1.2.3 Specialities<br />
1.2.3.1 Monomers for Waterborne Unsaturated Polyesters<br />
Waterborne unsaturated polyesters are used for wood coatings. They have<br />
UV-sensitive initiator systems. The basic constituents are selected from
Unsaturated Polyester Resins 11<br />
ethylene glycol, 1,2-propylene glycol, diethylene glycol, <strong>and</strong> tetrahydrophthalic<br />
anhydride, terephthalic acid, <strong>and</strong> trimellitic anhydride. 25 The vinyl<br />
monomer is trimethylolpropane diallyl ether. The UV-sensitive compound<br />
is 2-hydroxy-2-methylphenylpropane-1-one. When diluted with water, the<br />
resins exhibit a proper viscosity in the range of 2,500 cps. The cured products<br />
show good tensile properties <strong>and</strong> weatherability.<br />
Another method used to make unsaturated polyesters water soluble<br />
is to introduce polar hydrophilic groups such as carboxylic <strong>and</strong> sulfonic<br />
groups into the resin molecule, which ensures a good dispersibility in water.<br />
An example of such a compound is sodium 5-sulfonatoisophthalic<br />
acid. Instead of styrene, glycerol monoethers of allyl alcohol <strong>and</strong> unsaturated<br />
fatty alcohols are used as vinyl monomer. 26<br />
Unsaturated polyester resins diluted in water are used for particleboards<br />
<strong>and</strong> fiberboards. They are modified with acrylonitrile <strong>and</strong> also used<br />
as mixtures with urea/formaldehyde (UF) resins. A mixture of a UP resin<br />
<strong>and</strong> a UF resin allows the production of boards which have considerably<br />
higher mechanical properties than those bonded exclusively with UF resins.<br />
27<br />
1.2.3.2 Low Emission Modifiers<br />
Several methods have been proposed for reducing volatile organic compounds<br />
(VOCs) emissions:<br />
• Adding skin forming materials,<br />
• Replacement of the volatile monomer with a less volatile monomer,<br />
• Reduction in the amount of the monomer in the compositions, <strong>and</strong><br />
• Increasing the vinyl monomers by attaching them onto the polyester<br />
chain.<br />
Low Volatile Monomers. Styrene can be partly substituted for by low<br />
volatile monomers, such as bivalent metal salts of acrylic acid or methacrylic<br />
acid. Examples include zinc diacrylate, zinc dimethacrylate, calcium<br />
diacrylate, <strong>and</strong> calcium dimethacrylate. 28<br />
The metal salt monomer is typically a solid, <strong>and</strong> therefore has much<br />
lower vapor pressure than, e.g., styrene. The acrylate functionality copolymerizes<br />
readily with styrene. Due to the bivalent metal ions, the acrylates
12 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
act as crosslinkers of the ionomer type. Therefore, an additional crosslinking<br />
occurs in comparison to pure styrene.<br />
Acrylate-modified Unsaturated Polyesters. Acrylate-modified unsaturated<br />
polyesters may be used for low-viscosity resins <strong>and</strong> resins with<br />
low emission of volatile monomers. In commercially available unsaturated<br />
polyester resin applications, up to 50% of styrene or other vinyl monomers<br />
are used. During curing some of the organic monomer is usually lost to<br />
the atmosphere, which causes occupational safety hazards <strong>and</strong> an environmental<br />
problem.<br />
Tailoring the polyester by synthesizing branched structures <strong>and</strong> incorporating<br />
additional vinyl unsaturations has been proposed. The diol<br />
alcohols used for condensation may be partly replaced by glycidyl compounds<br />
in order to obtain low molecular weight methacrylate or acrylatemodified<br />
or terminated polyesters. 29 Suitable glycidyl compounds include<br />
glycidyl methacrylate <strong>and</strong> glycidyl acrylate. Not more than 60 mol-% of<br />
the alcohols can be replaced by glycidyl compounds.<br />
23, 30<br />
These polyesters have low viscosities because of the branched structures.<br />
In addition to the maleic or fumaric units, they bear additional unsaturations<br />
resulting from the pending reactive acrylate or methacrylate<br />
moieties. For this reason these types need less vinyl monomer (styrene)<br />
to increase the crosslinking density of the cured product. The increased<br />
unsaturation results in a higher reactivity, which in turn leads to an increase<br />
in heat distortion temperature <strong>and</strong> better corrosion resistance, good<br />
pigmentability <strong>and</strong> excellent mechanical <strong>and</strong> physical properties. 31 Such<br />
resins are therefore suitable as basic resins in gel coats.<br />
1.2.3.3 Epoxide-based Unsaturated Polyesters<br />
Epoxide-based unsaturated polyesters are obtained from the reaction of<br />
half esters of maleic anhydride of fumaric acid with epoxy groups from<br />
epoxide resins. For example, n-hexanol reacts easily with maleic anhydride<br />
to form acidic hexyl maleate. This half ester is then used for the addition<br />
reaction with the epoxy resin. 32<br />
Allyl alcohol in the unsaturated resins enhances their properties. The<br />
glass-transition temperatures of the epoxy fumarate resins exceed 100°C.<br />
The glass-transition temperatures epoxy maleates are higher than 70°C.<br />
The resins have good chemical resistance. 33
Unsaturated Polyester Resins 13<br />
HO<br />
C<br />
O<br />
O<br />
O<br />
OH<br />
C<br />
NH<br />
C<br />
Figure 1.7: o-Carboxy phthalanilic acid 13<br />
1.2.3.4 Isocyanates<br />
Isocyanates, such as toluene diisocyanate can be added to a formulated<br />
resin, such as polyester plus vinyl monomer. The gelation times increase<br />
with the concentration of toluene diisocyanate.<br />
Also the viscosity increases strongly. Resins with only 3% of toluene<br />
diisocyanate are thixotropic. 34 An increase in the viscosity is highly<br />
undesirable.<br />
1.2.3.5 o-Carboxy phthalanilic acid<br />
A new acid monomer, o-carboxy phthalanilic acid, c.f., Figure 1.7, has<br />
been synthesized from o-aminobenzoic acid with phthalic anhydride. This<br />
monomer was condensed with different acids <strong>and</strong> glycols to prepare unsaturated<br />
polyesters. These polyesters were admixed with styrene <strong>and</strong> cured.<br />
The final materials were extensively characterized.<br />
13, 35<br />
It was found that the styrene/poly(1,2-propylene-maleate-o-carboxy<br />
phthalanilate) polyester resin has the highest compressive strength value<br />
<strong>and</strong> the best chemical resistance <strong>and</strong> physical properties among the materials<br />
under investigation.<br />
1.2.4 Synthesis<br />
The synthesis of unsaturated polyesters occurs either by a bulk condensation<br />
or by azeotropic condensation. General purpose polyesters can be condensed<br />
by bulk condensation, whereas more sensitive components need the<br />
azeotropic condensation technique, which can be performed at lower temperatures.<br />
The synthesis in the laboratory scale does not differ significantly<br />
from the commercial procedure.
14 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
1.2.4.1 Kinetics of Polyesterification<br />
The kinetics of polyesterification have been modelled. In the models,<br />
the asymmetry of 1,2-propylene glycol was taken into account, because<br />
it bears a primary <strong>and</strong> secondary hydroxyl group. The reactivities of these<br />
hydroxyl groups differ by a factor of 2.6. The relative reactivity of maleic<br />
<strong>and</strong> phthalic anhydride towards 1,2-propylene glycol, after the ring opening<br />
of both anhydrides is complete, increases from ca. 1.7 to 2.3 when the<br />
temperature is increased from 160 to 220°C. 36<br />
The rate constants <strong>and</strong> Arrhenius parameters are estimated by fitting<br />
the calculated conversion of the acid with time to the experimental<br />
data over the entire range of conversion. For the copolyesterification reactions<br />
involving two acids, a cross-catalysis model is used. 37 The agreement<br />
between model predictions <strong>and</strong> experimental data has been proved<br />
to be satisfactory. For example, the energy of activation for the condensation<br />
reaction of 2-methyl-1,3-propanediol (MPD) with maleic anhydride<br />
was obtained to 65 kJ/mol, <strong>and</strong> with phthalic anhydride 82 kJ/mol was<br />
obtained.<br />
1.2.4.2 Sequence Distribution of Double Bonds<br />
The polycondensate formed by the melt condensation process of maleic<br />
anhydride, phthalic anhydride, <strong>and</strong> 1,2-propylene glycol in the absence of<br />
a transesterification catalyst has a non-r<strong>and</strong>om structure with a tendency towards<br />
blockiness. On the other h<strong>and</strong>, the distribution of unsaturated units<br />
in the unsaturated polyester influences the curing kinetics with the styrene<br />
monomer. Segments containing double bonds close together appear<br />
to lower the reactivity of the resin due to steric hindrance. This is suggested<br />
by the fact that the rate of cure <strong>and</strong> the final degree of conversion<br />
increase as the average sequence length of the maleic units decreases. Due<br />
to the influence of the sequence length distribution on the reactivity, the<br />
reactivity of unsaturated polyester resins may be tailored by sophisticated<br />
condensation methods.<br />
Methods to calculate the distributions have been worked out.<br />
38, 39<br />
Monte Carlo methods can be used to investigate the effects of the various<br />
rate constants <strong>and</strong> stoichiometry of the reactants. Also, structural asymmetry<br />
of the diol component <strong>and</strong> the influence of the dynamics of the ring<br />
opening of the anhydride is considered.
Unsaturated Polyester Resins 15<br />
O<br />
CH 3<br />
O + CH CH 2<br />
OH OH<br />
O<br />
O<br />
OH<br />
O CH CH 2<br />
O CH 3<br />
OH<br />
Figure 1.8: Reaction of Maleic anhydride with 1,2-Propanediol<br />
1.2.5 Manufacture<br />
Unsaturated polyesters are still produced in batch. Continuous processes<br />
have been invented, but are not widespread. Most common is a cylindrical<br />
batch reactor equipped with stirrer, condenser, <strong>and</strong> a jacket heater. Thus<br />
the synthesis in laboratory <strong>and</strong> in industry is very similar. The typical size<br />
of such reactors is between 2 <strong>and</strong> 10 m 3 .<br />
We now illustrate a typical synthesis of an unsaturated polyester.<br />
The reactor is filled at the room temperature with the glycol, in slight excess<br />
to compensate the losses during the condensation. Losses occur because<br />
of the volatility of the glycol, but also due to side reactions. The glycol<br />
may eliminate water at elevated temperatures. Then maleic anhydride<br />
<strong>and</strong> phthalic anhydride are charged to the reactor. Typical for a general<br />
purpose unsaturated polyester resin is a ratio of 1 mol maleic anhydride, 1<br />
mol phthalic anhydride, <strong>and</strong> 1.1 mol 1,2-propylene glycol. Further, other<br />
components, such as adhesion promoters, can be added.<br />
The reactor is sparged with nitrogen <strong>and</strong> slowly heated. At ca. 90°C<br />
the anhydrides react with the glycol in an exothermic reaction. This is the<br />
initial step of the polyreaction, shown in Figure 1.8. At the end of the<br />
exothermic reaction a condensation catalyst may be added.<br />
Catalysts such as lead dioxide, p-toluenesulfonic acid, <strong>and</strong> zinc acetate<br />
40 affect the final color of the polyester <strong>and</strong> the kinetics of curing.<br />
Temperature is raised carefully up to 200°C, so that the temperature<br />
of the distillate never exceeds ca. 102 to 105°C. Otherwise the glycol<br />
distills out. The reaction continues under nitrogen or carbon dioxide atmosphere.<br />
The sparging is helpful for removing the water. Traces of oxygen<br />
could cause coloration. The coloration emerges due to multiple conjugated<br />
double bonds. Maleic anhydride is helpful in preventing coloration,<br />
because the series of conjugated double bonds are interrupted by a Diels-<br />
Alder reaction. In the case of sensitive components, e.g., diethylene glycol,
16 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
even small amounts of oxygen can cause gelling during the condensation<br />
reaction.<br />
There are certain variations of water removal. Simply sparging with<br />
inert gas is referred to as the melt condensation technique. In the case of<br />
thermal sensitive polyesters, the water may be removed by the azeotrope<br />
technique. Toluene or xylene is added to the reaction mixture. Both compounds<br />
form an azeotrope with water. During reflux, water separates from<br />
the aromatic solvent <strong>and</strong> can be collected. In the final stage, the aromatic<br />
solvent must be removed either by enhanced sparging or under vacuum.<br />
The azeotrope technique is in general preferred, because condensation proceeds<br />
faster than in the case of melt condensation.<br />
Vacuum also can be used to remove the water, although this technique<br />
is used only rarely for unsaturated polyesters because of the risk of<br />
removal of the glycol.<br />
At early stages, the progress of the condensation reaction can be<br />
controlled via the amount of water removed. In the final stage, this method<br />
is not sufficiently accurate <strong>and</strong> the progress is monitored via the acid number.<br />
Samples are withdrawn from the reactor <strong>and</strong> are titrated with alcoholic<br />
potassium hydroxide (KOH) solution. The acid number is expressed in<br />
milligrams KOH per gram of resin. Even though other methods for the determination<br />
of the molecular weight are common in other fields, the control<br />
of the acid number is the quickest method to follow the reaction.<br />
The kinetics of self-catalyzed polyesterification reactions follows a<br />
third-order kinetic law. Acid catalyzed esterification reactions follow a<br />
second-order kinetics. In the final stage of the reaction, the reciprocal of<br />
the acid number is linear with time.<br />
General purpose unsaturated polyester resins are condensed down<br />
to an acid number of around 50 mgKOH/g resin. This corresponds to a<br />
molecular weight of approximately 1000 Dalton. After this acid number<br />
has been reached, some additives are added, in particular polymerization<br />
inhibitors, e.g., hydroquinone, <strong>and</strong> the polyester is cooled down, to initiate<br />
the mixing with styrene. The polyester should be cooled down to the lowest<br />
possible temperature. In any case the temperature of the polyester should<br />
be below the boiling point of the vinyl monomer. There are two limiting<br />
issues:<br />
1. If the polyester is too hot, after mixing with the vinyl monomer a<br />
preliminary curing may take place. In the worst case the resin may<br />
gel.
Unsaturated Polyester Resins 17<br />
Table 1.3: Inhibitors <strong>and</strong> Retarders for Unsaturated Polyester Resins<br />
Inhibitor<br />
Hydroquinone<br />
1,4-Naphthoquinone<br />
p-Benzoquinone<br />
Chloranil<br />
Catechol<br />
Picric acid<br />
Retarder<br />
2,4-Pentanedione<br />
2. If the polyester is too cold, its viscosity becomes too high, which<br />
jeopardizes the mixing process.<br />
Mixing can occur in several ways: either the polyester is poured into<br />
styrene under vigorous stirring, or under continuous mixing, or the styrene<br />
is poured into the polyester. The last method is preferred in the laboratory.<br />
After mixing, the polyester resin is then cooled down to room temperature<br />
as quickly as possible. Finally some special additives are added, such as<br />
promoter for preaccelerated resin composition. An unsaturated polyester<br />
resin is not miscible in all ratios with styrene. If an excess of styrene is<br />
added, a two-phase system will emerge.<br />
The resins have a slightly yellow color, mainly due to the inhibitor.<br />
The final product is filtered, if necessary, <strong>and</strong> poured into vats or cans.<br />
1.3 SPECIAL ADDITIVES<br />
1.3.1 Inhibitors<br />
There is a difference between inhibitors <strong>and</strong> retarders. Inhibitors stop the<br />
polymerization completely, whereas retarders slow down the polymerization<br />
rate. Inhibitors influence the polymerization characteristics. They act<br />
in two ways:<br />
1. Increasing the storage time<br />
2. Decreasing the exothermic peak during curing<br />
Common inhibitors are listed in Table 1.3. Inhibitors are used to increase<br />
the storage time, <strong>and</strong> also to increase the pot life time. Sometimes a combination<br />
of two or more inhibitors is used, since some types of inhibitors act<br />
more specifically on the storage time <strong>and</strong> others influence the pot life time.
18 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
The storage time of an unsaturated polyester resin increases with<br />
the amount of inhibitor. Storage at high temperatures decreases the possible<br />
shelf life. On the other h<strong>and</strong>, high doses of inhibitor detrimentally<br />
influence the curing of the resin. Higher amounts of radical initiators are<br />
required in the presence of high doses of inhibitors. The exothermic peak<br />
during curing is reduced. This influences the degree of monomer conversion.<br />
A high degree of conversion is needed to have optimal properties.<br />
1.3.2 Thickeners<br />
1.3.2.1 Multivalent Salts<br />
For sheet molding compounds <strong>and</strong> bulk molding compounds, the resins are<br />
thickened. This can be achieved particularly with MgO, at a concentration<br />
of about 5%.<br />
It is believed that it first interacts with the carboxylic acid group on<br />
chains. Then a complex is formed with the salt formed <strong>and</strong> the carboxylic<br />
acid groups of other chains, leading to an increase in viscosity. The maximum<br />
hardness is achieved at 2% MgO with an increase from 190 MPa to<br />
340 MPa for the specimen cured at room temperature. High temperature<br />
curing decreases hardness.<br />
1.3.2.2 Thixotropic Additives<br />
For gel coat applications, fumed silica, precipitated silica or an inorganic<br />
clay can be used. Hectorite <strong>and</strong> other clays can be modified by alkyl quaternary<br />
ammonium salts such as di(hydrogenated tallow) ammonium chloride.<br />
These organoclays are used in thixotropic unsaturated polyester resin<br />
systems. 41<br />
1.3.3 Emission Suppressants<br />
If a polyester is exposed to open air during curing, the vinyl monomer can<br />
easily evaporate. This leads to a change in the composition <strong>and</strong> thus to<br />
a change in the glass transition temperature of the final product. 42 Still<br />
more undesirable is the emission of potentially toxic compounds. There<br />
are several approaches to achieving products with low emission rates.<br />
The earliest approach has been the use of a suppressant which reduces<br />
the loss of volatile organic compounds. The suppressants are often
Unsaturated Polyester Resins 19<br />
waxes. The wax-based products are of a limited comparability with the<br />
polyester resin. The wax-based suppressants separate from the system during<br />
polymerization or curing, forming a surface layer which serves as a<br />
barrier to volatile emissions.<br />
For example, a paraffin wax having a melting point of about 60°C<br />
significantly improves the styrene emission results. Waxes with a different<br />
melting point from this temperature will not perform adequately at the low<br />
concentrations necessary to maintain good bonding <strong>and</strong> physical properties<br />
while inhibiting the styrene emissions. 43 The waxy surface layer must be<br />
removed before the next layer can be applied, because waxes are likely to<br />
cause a reduction in the interlaminar adhesion bond strength of laminating<br />
layers.<br />
Suppressants selected from polyethers, polyether block copolymers,<br />
alkoxylated alcohols, alkoxylated fatty acids or polysiloxanes show a suppression<br />
of the emission as well <strong>and</strong> better bonding properties. 44–46 Unsaturated<br />
polyesters that contain α,β-unsaturated dicarboxylic acid residues<br />
<strong>and</strong> allyl ether or polyalkylene glycol residues (so-called gloss polyesters)<br />
require no paraffin for curing the surface of a coating, because the ether<br />
groups initiate an autoxidative drying process. 47<br />
1.3.4 Fillers<br />
Examples for fillers include calcium carbonate powder, clay, alumina powder,<br />
silica s<strong>and</strong> powder, talc, barium sulfate, silica powder, glass powder,<br />
glass beads, mica, aluminum hydroxide, cellulose yarn, silica s<strong>and</strong>, river<br />
s<strong>and</strong>, white marble, marble scrap, <strong>and</strong> crushed stone. In the case of glass<br />
powder, aluminum hydroxide, <strong>and</strong> barium sulfate the translucency is imparted<br />
on curing. 48 Common fillers are listed in Table 1.4. Fillers reduce<br />
the cost <strong>and</strong> change certain mechanical properties of the cured materials.<br />
1.3.4.1 Inorganic Fillers<br />
Bentonite. Ca-bentonite is used in the formulation of unsaturated polyester-based<br />
composite materials. Increasing the filler content, at a constant<br />
styrene/polyester ratio, improves the properties of composites. Maximum<br />
values of compressive strength, hardness, <strong>and</strong> thermal conductivity of composites<br />
are observed at about 22.7% of styrene, whereas the water absorption<br />
capacity was a minimum at a styrene content of 32.8%. 49
20 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 1.4: Fillers for Unsaturated Polyester Resins<br />
Filler<br />
Reference<br />
Bentonite<br />
49<br />
Calcium carbonate<br />
50<br />
Clay<br />
51<br />
Glass beads<br />
Flyash<br />
52<br />
Woodflour<br />
53<br />
Rubber particles<br />
54<br />
Nanocomposites<br />
55–57<br />
Montmorillonite. Sodium montmorillonite <strong>and</strong> organically modified<br />
montmorillonite (MMT) were tested as reinforcing agents. Montmorillonite<br />
increases the glass transition temperatures. At 3-5% modified montmorillonite<br />
content, the tensile modulus, tensile strength, flexural modulus <strong>and</strong><br />
flexural strength values showed a maximum, whereas the impact strength<br />
exhibited a minimum. Adding only 3% of organically modified montmorillonite<br />
improved the flexural modulus of an unsaturated polyester by 35%.<br />
The tensile modulus of unsaturated polyester was also improved by 17%<br />
at 5% of montmorillonite. 51<br />
Instead of styrene, 2-hydroxypropyl acrylate (HPA) as a reactive diluent<br />
has been examined in preparing an unsaturated polyester/montmorillonite<br />
nanocomposite. 58 The functionalization of MMT can be achieved<br />
with polymerizable cationic surfactants, e.g., with vinylbenzyldodecyldimethyl<br />
ammonium chloride (VDAC) or vinylbenzyloctadecyldimethyl ammonium<br />
chloride (VOAC). Polymerizable organophilic clays have been<br />
prepared by exchanging the sodium ions of MMT with these polymerizable<br />
cationic surfactants. 59 With an unsaturated polyester, nanocomposites<br />
consisting of UP <strong>and</strong> clay were prepared. The dispersion of organoclays<br />
in UP caused gel formation. In the UP/VDAC/MMT system, intercalated<br />
nanocomposites were found, while in the UP/VOAC/MMT system partially<br />
exfoliated nanocomposites were observed.<br />
When the content of organophilic montmorillonite is between 25%<br />
<strong>and</strong> 5%, the mechanical properties, such as the tensile strength, the impact<br />
strength, the heat resistance, <strong>and</strong> the swelling resistance of the hybrid<br />
are enhanced. The properties are better than those of composites prepared<br />
with pristine or non-polymerizable quaternary ammonium-modified montmorillonite.<br />
60
Unsaturated Polyester Resins 21<br />
Flyash. Flyash is an inexpensive material that can reduce the overall<br />
cost of the composite if used as filler for unsaturated polyester resin. A<br />
flyash-filled resin was found to have a higher flexural modulus than those<br />
of a calcium carbonate-filled polyester resin <strong>and</strong> an unfilled resin. Flyash<br />
was found to have poor chemical resistances but good saltwater, alkali,<br />
weathering, <strong>and</strong> freeze-thaw resistances. 52<br />
An enhancement of the tensile strength, flexural strength, <strong>and</strong> impact<br />
strength is observed when the flyash is surface-treated with silane coupling<br />
agents. 61<br />
1.3.4.2 Wood flour<br />
Plant-based fillers like sawdust, wood flour <strong>and</strong> others are utilized because<br />
of their low density, <strong>and</strong> their relatively good mechanical properties <strong>and</strong><br />
reactive surface. The main disadvantage is the hygroscopicity 62 <strong>and</strong> the<br />
difficulties in achieving acceptable dispersion in a polymeric matrix.<br />
Surface modification of these materials can help reduce these problems.<br />
Wood flour can be chemically modified with maleic anhydride to<br />
improve the dispersion properties <strong>and</strong> adhesion to the matrix resin. This<br />
treatment decreases the hygroscopicity, but excessive esterification has to<br />
be avoided, because it leads to the deterioration of the wood flour, adversely<br />
affecting its mechanical properties. 53<br />
The incorporation of wood flour into the resin increases the compression<br />
modulus <strong>and</strong> the yield stress but decreases the ultimate deformation<br />
<strong>and</strong> toughness in all cases.<br />
Thermogravimetric analysis of wood flour indicates changes in the<br />
wood structure occur as a consequence of chemical modifications. Alkaline<br />
treatment reduces the thermal stability of the wood flour <strong>and</strong> produces<br />
a large char yield. In composites a thermal interaction between fillers <strong>and</strong><br />
matrix is observed. Thermal degradation of the composites begins at higher<br />
temperature than the neat wood flours. 63<br />
1.3.4.3 Rubber<br />
Rubber particles toughen the materials.<br />
54, 64<br />
They act also as low-profile<br />
additives. A low-profile additive, in general, diminishes shrinking in the<br />
course of curing.
22 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Toughening. Rubbers with functional groups have been tested in blends<br />
of unsaturated polyesters with respect to improving the mechanical properties.<br />
In particular, functional rubbers such as hydroxy terminated poly-<br />
(butadiene), epoxidized natural rubber, hydroxy-terminated natural rubber,<br />
<strong>and</strong> maleated nitrile rubber were tested. The performance of a maleic anhydride-grafted-nitrile<br />
rubber is superior to all other rubbers studied. The improvement<br />
in toughness, impact resistance, <strong>and</strong> tensile strength is achieved<br />
without jeopardizing other properties. 65<br />
Rubber as Low-profile Additive. A low-profile additive consisting of<br />
a styrene-butadiene rubber solution is prepared by heating styrene with<br />
hydroquinone up to 50°C. Into this liquid a styrene-butadiene rubber is<br />
dissolved to obtain a resin solution having a solid content of 35%. This<br />
solution is taken as a low-profile additive. 66<br />
1.3.4.4 Nanocomposites<br />
Only a few nanocomposite materials are commercially available <strong>and</strong> these<br />
materials are very expensive. In order to make a successful nanocomposite,<br />
it is very important to be able to disperse the filler material thoroughly<br />
throughout the matrix to maximize the interaction between the intermixed<br />
phases.<br />
Titanium dioxide. Titanium dioxide nanoparticles with 36 nm average<br />
diameter have been investigated. The nanoparticles have to be dispersed<br />
by direct ultrasonification. 55 The presence of the nanoparticles has<br />
a significant effect on the quasi-static fracture toughness. Even at small<br />
volume fractions an increase in toughness is observed. The changes in<br />
quasi-static material properties in tension <strong>and</strong> compression with increasing<br />
volume fraction of the nanoparticles are small due to the weak interfacial<br />
bonding between the matrix <strong>and</strong> the filler. The dynamic fracture toughness<br />
is higher than quasi-static fracture toughness. Quite similar experimental<br />
results have been presented by another group. 67 Titanium dioxide nanoparticles<br />
can also be bound by chemical reaction to the polyester itself. 68<br />
Aluminum Oxide. It was observed that the addition of untreated, Al 2 O 3<br />
particles does not result in an enhanced fracture toughness. Instead, the<br />
fracture toughness decreases. 56, 57 However, adding an appropriate amount
Unsaturated Polyester Resins 23<br />
Table 1.5: Reinforcing Materials for Unsaturated Polyesters<br />
Fiber<br />
Reference<br />
Glass fibers<br />
Jute<br />
69<br />
Sisal<br />
70<br />
Hemp<br />
71<br />
Wollastonite<br />
70<br />
Barium titanate<br />
72<br />
of (3-methacryloxypropyl)trimethoxysilane to the liquid polyester resin<br />
during particle dispersion process leads to a significant enhancement of the<br />
fracture toughness due to the crack trapping mechanism being promoted by<br />
strong particle-matrix adhesion.<br />
For example, the addition of 4.5% volume fraction of treated Al 2 O 3<br />
particles results in a nearly 100% increase in the fracture toughness of the<br />
unsaturated polyester.<br />
1.3.5 Reinforcing Materials<br />
Suitable reinforcing materials are shown in Table 1.5. The application of<br />
reinforcement fibers is strongly governed by the relation of the price of<br />
matrix resin <strong>and</strong> fiber. Therefore, expensive fibers, such as carbon fiber,<br />
are usually used with epoxide resins, not with unsaturated polyester resins.<br />
If the fiber is expensive <strong>and</strong> has superior properties, then the matrix resin<br />
should have superior properties.<br />
1.3.5.1 Glass Fibers<br />
The most common “fillers” are reinforcing materials, like glass fibers. Because<br />
of the unavoidable shrinking during curing, interfacial stresses between<br />
resin <strong>and</strong> glass fiber arise that lower the adhesion forces.<br />
To enhance the adhesion, glass fibers are surface-modified. Silane<br />
coupling agents such as (3-methacryloxypropyl)trimethoxysilane <strong>and</strong><br />
(3-aminopropyl)triethoxysilane are preferably used.<br />
In the case of (3-methacryloxypropyl)trimethoxysilane the pendent<br />
double bonds may take part in the curing reaction; thus chemical linkages<br />
between resin <strong>and</strong> glass surface are established.
24 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
The surface free energy <strong>and</strong> the mechanical interfacial properties<br />
especially showed the maximum value for 0.4% silane coupling agent.<br />
73, 74<br />
In an E-glass/vinylester composite it was observed that the fibers<br />
significantly inhibit the final conversion. 75<br />
1.3.5.2 Wollastonite<br />
A suitable coupling agent for wollastonite is (3-methacryloxypropyl)trimethoxysilane.<br />
In such a treated wollastonite-unsaturated polyester composite,<br />
the tensile <strong>and</strong> flexural strength increase initially with the wollastonite<br />
content <strong>and</strong> then decrease. The flexural strength reaches an optimum<br />
value at 30% wollastonite content, whereas the tensile strength reaches an<br />
optimum point at 50% wollastonite content. 70<br />
1.3.5.3 Carbon Fibers<br />
Reports on carbon fiber reinforced polyester are rare. 76 Carbon fibers have<br />
mainly been used in aerospace with epoxide resins or high temperature<br />
thermoplastics, whereas polyesters have found application in large-volume<br />
<strong>and</strong> low-cost applications with primarily glass fibers as reinforcement. The<br />
combination of carbon fibers <strong>and</strong> polyester matrix is becoming more attractive<br />
as the cost of carbon fibers decreases. In comparison to epoxide<br />
resins, unsaturated polyester exhibits a relatively low viscosity. This property<br />
makes them well suited for the manufacture of large structures. 77<br />
The interfacial shear strength with untreated carbon fibers increases<br />
with increasing degree of unsaturation of the polyester. The unsaturation is<br />
adjusted by the amount of maleic anhydride in the feed. This is explained<br />
by a contribution of chemical bonding of the double bonds in the polymer<br />
to the functional groups of the carbon fiber surface. 77<br />
1.3.5.4 Natural Fibers<br />
Agrowastes <strong>and</strong> biomass materials, e.g., sawdust, wood fibers, sisal, bagasse,<br />
etc. are slowly penetrating the reinforced plastics market, presently<br />
dominated by glass fibers <strong>and</strong> other mineral reinforcements. These fillers<br />
have very good mechanical properties <strong>and</strong> low density, <strong>and</strong> are loaded into<br />
polymeric resin matrices to make useful structural composite materials. 62
Unsaturated Polyester Resins 25<br />
Jute. Jute as reinforcing fiber is particularly significant from an economic<br />
point of view. On a weight <strong>and</strong> cost basis, bleached jute fibers are claimed<br />
to have better reinforcement properties than other fibers. 69<br />
Sisal. Sisal fiber is a vegetable fiber having specific strength <strong>and</strong> stiffness<br />
that compare well with those of glass fiber. Most synthetic resins are,<br />
however, more expensive than the sisal fiber, making these composites less<br />
attractive for low-technology applications. Therefore, for sisal fibers naturally<br />
occurring resol-type resins, cashew nut shell liquid is an attractive<br />
alternative. 78<br />
For unsaturated polyester composites the surface treatment of sisal<br />
fibers is done with neopentyl(diallyl)oxy tri(dioctyl)pyrophosphatotitanate<br />
as the coupling agent.<br />
70, 79<br />
In a sisal/wollastonite reinforcing system for<br />
unsaturated polyester resins, the tensile strength <strong>and</strong> the flexural strength<br />
drop with increasing sisal content.<br />
Sisal composites with unsaturated polyesters can be formulated to<br />
be flame retarded using decabromodiphenyloxide <strong>and</strong> antimony trioxide to<br />
reach a satisfactory high state of flame retardancy. 80<br />
1.3.6 Mold Release Agents<br />
Mold release agents are needed for the molding processes, i.e., for the<br />
manufacture of bulk molding compounds <strong>and</strong> sheet molding compounds.<br />
There are two classes of mold release agents:<br />
1. External mold release agents,<br />
2. Internal mold release agents.<br />
External mold release agents are applied directly to the mold. This<br />
procedure increases the manufacturing time <strong>and</strong> must be repeated every<br />
one to five parts. In addition, the mold release agent builds up on the mold,<br />
so the mold must be cleaned periodically with a solvent or washing agent.<br />
This is costly <strong>and</strong> time consuming.<br />
Internal mold release agents are added directly into the molding<br />
compound. Since they do not have to be continuously reapplied to the<br />
mold, internal mold release agents increase productivity <strong>and</strong> reduce cost.<br />
There are mostly internal mold release agents, e.g., metal soaps, amine<br />
carboxylates, amides, etc. Zinc stearate acts by exuding to the surface
26 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
of the molding compound, thereby contacting the mold <strong>and</strong> providing lubrication<br />
at the mold surface to permit release. Liquid mold release agents<br />
are liquid zinc salts <strong>and</strong> phosphate esters <strong>and</strong> higher fatty acid amines. 81<br />
The amine salts are obtained simply by neutralizing the acids with appropriate<br />
amines.<br />
1.3.7 Low-profile Additives<br />
Low-profile additives (LPA) reduce the shrinking of the cured products.<br />
Shrinking causes internal voids <strong>and</strong> reduced surface quality. Thermoplastic<br />
resins are added to reduce shrinking, e.g., poly(vinyl acetate). This<br />
additive absorbs some styrene in the early stages of curing. When the temperature<br />
is increased in the course of curing, the styrene eventually evaporates<br />
<strong>and</strong> consequently a counter pressure is formed which counterbalances<br />
the shrinking.<br />
The successful performance of low-profile additives depends essentially<br />
on the phase separation phenomena in the course of curing, c.f. Section<br />
1.4.4.2.<br />
The effects of poly(vinyl acetate), poly(vinyl chloride-co-vinyl acetate),<br />
<strong>and</strong> poly(vinyl chloride-co-vinyl acetate-co-maleic anhydride), have<br />
been studied. 82, 83 The curing rate decreases with an increase of the molecular<br />
weight of the low-profile additive which causes the chain entanglement<br />
effect. The plasticizing effect is reduced with an increase in the molecular<br />
weight of the low-profile additive. 84<br />
Low-profile additives with higher molecular weight <strong>and</strong> lower content<br />
of additive seem to work better under low-temperature curing conditions.<br />
85 <strong>Polymers</strong> from the acrylic group have been tested as low-profile additives.<br />
In particular, binary copolymers from methyl methacrylate <strong>and</strong> n-<br />
butyl acrylate, <strong>and</strong> ternary copolymers from methyl methacrylate, n-butyl<br />
acrylate, <strong>and</strong> maleic anhydride have been studied. 86, 87 The volume fraction<br />
of microvoids generated during the curing process is governed by the<br />
stiffness of the UP resin, the compatibility of the uncured ST/UP/LPA systems,<br />
<strong>and</strong> the glass-transition temperature of the low-profile additive. A<br />
good volume shrinkage control can be achieved by raising the curing temperature<br />
slowly to allow sufficient time for phase separation, <strong>and</strong> going to<br />
a high final temperature to allow the formation of microvoids. 88<br />
Dilatometric studies in the course of curing of a low-profile resin
Unsaturated Polyester Resins 27<br />
containing poly(vinyl acetate) 89 have revealed that there are two transition<br />
points in both volume <strong>and</strong> morphological changes in the course of curing.<br />
The thermoplastics start to be effective on shrinkage control at the<br />
first transition point when the low-profile additive-rich phase <strong>and</strong> the unsaturated<br />
polyester resin-rich phase become co-continuous. At the second<br />
transition point when the fusion among the particulate structures is severe,<br />
the shrinkage control effect vanishes.<br />
The relative rate of polymerization in the two phases plays an important<br />
role in shrinkage control. Instead of poly(vinyl acetate) a copolymer<br />
with acrylic acid or itaconic acid should have better properties as a<br />
low-profile additive. This is based on the assumption that the presence of<br />
acid groups on the copolymer chain changes the selectivity of the cobalt<br />
promoter, <strong>and</strong> therefore, the relative reaction rate in the thermoplastic-rich<br />
<strong>and</strong> the unsaturated polyester resin-rich phases during polymerization.<br />
Itaconic acid is about twice as acidic as acrylic acid <strong>and</strong> more reactive<br />
than maleic acid or fumaric acid. The two carboxyl groups allow the<br />
introduction of larger amounts of acidity into the copolymer even at rather<br />
low comonomer concentrations in comparison to acrylic acid. The monoester<br />
of 2-hydroxyethyl acrylate <strong>and</strong> tetrachlorophthalic anhydride also has<br />
been proposed as a comonomer. The acidity of tetrachlorophthalic anhydride<br />
is much stronger than that of itaconic acid because of the four chloro<br />
substituents in its structure.<br />
Samples with an acid-modified low-profile additive showed an earlier<br />
volume expansion during curing, as a result of faster reaction in the<br />
low-profile additive-rich phase. 90<br />
The relative reaction rate in the two phases can be controlled in<br />
addition to the selectivity control by the low-profile additive in a reverse<br />
manner, i.e., by the addition of secondary vinylic comonomers <strong>and</strong> special<br />
promoters. Secondary monomers, such as divinylbenzene <strong>and</strong> trimethylolpropane<br />
trimethacrylate, were added to the formulation. 2,4-Pent<strong>and</strong>ione<br />
was chosen as co-promoter. 91 In fact, the combination of trimethylolpropane<br />
trimethacrylate <strong>and</strong> 2,4-pent<strong>and</strong>ione increased the reaction rate in the<br />
low-profile rich-phase.<br />
Methyl methacrylate was tested as a secondary monomer. 92 At a low<br />
ratio of methyl methacrylate to styrene, the amount of residual styrene decreases<br />
<strong>and</strong> the volume shrinkage of the resin system remains unchanged.<br />
However, at a high ratio of methyl methacrylate to styrene, the amount of<br />
residual styrene can be substantially reduced. This advantageous behav-
28 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
ior occurs because of the monomer reactivity ratios. However, the study<br />
of shrinkage shows that methyl methacrylate has a negative effect on the<br />
shrinkage control.<br />
Styrene has a polymerization shrinkage of 15% <strong>and</strong> methyl methacrylate<br />
has a shrinkage of 20%. Therefore, the addition of methyl methacrylate<br />
contributes to a larger volume shrinkage. The performance of a<br />
low-profile additive becomes less effective when the molar ratio of methyl<br />
methacrylate to styrene exceeds 0.1.<br />
A dual initiator system, i.e., methylethylketone peroxide/tert-butylperoxybenzoate,<br />
was used in combination with cobalt octoate as a promoter.<br />
tert-Butylperoxybenzoate cannot be considered a low temperature<br />
initiator because the reaction temperature needs to reach almost 90°C<br />
to ensure the proper progress of the reaction. On the other h<strong>and</strong>, tertbutylperoxybenzoate<br />
is more active compared to methylethylketone peroxide<br />
at high temperatures, because the latter completely decomposes.<br />
tert-Butylperoxybenzoate is therefore a good initiator to finish the reaction.<br />
Volume shrinkage measurements of the resin system initiated with<br />
dual initiators revealed that a good performance of the low-profile additive<br />
was achieved at low temperatures (e.g., 35°C) <strong>and</strong> high temperatures<br />
(100°C) but not at intermediate temperatures. 93<br />
It was found that in bulk molding compounds calcium stearate, which<br />
is primarily used as an internal mold release agent, is active as a low-profile<br />
additive. 94 Even when added in small quantities, some internal mold<br />
release agents may provoke the formation of a polyester-rich phase in the<br />
form of spherical globules ca. 60 µm.<br />
1.3.8 Interpenetrating Polymer Networks<br />
An interpenetrating polymer network is a mixture of two or more polymers<br />
that are not necessarily independently crosslinked. If another polymer that<br />
is capable of crosslinking separately is added to an unsaturated polyester<br />
resin, the physical properties can be enhanced dramatically. Other special<br />
types of such systems are also addressed as hybrid systems.<br />
1.3.8.1 Polyurethanes<br />
For example, besides the unsaturated polyester resin, compounds that simultaneously<br />
form a crosslinkable polyurethane are added, such as poly-
Unsaturated Polyester Resins 29<br />
glycols <strong>and</strong> diisocyanates. 95<br />
The rate of reaction of one component might be expected to be reduced<br />
due to the dilutional effects by the other components. 96 However,<br />
during free radical polymerization, the reaction may become diffusion<br />
controlled <strong>and</strong> a Trommsdorff effect emerges. The Trommsdorff effect<br />
consists of a self-acceleration of the overall rate of polymerization. When<br />
the polymerizing bulk becomes more viscous as the concentration of polymer<br />
increases, the mutual deactivation of the growing radicals is hindered,<br />
whereas the other elementary reaction rates, such as initiation <strong>and</strong> propagation,<br />
remain constant.<br />
For an unsaturated polyester resin – polyurethane system, the rate of<br />
the curing process increased substantially in comparison to the pure homopolymers.<br />
Collateral reactions between the polyurethane isocyanate groups<br />
<strong>and</strong> the terminal unsaturated polyester carboxyl groups were suggested that<br />
may lead to the formation of amines, c.f. Eq. 1.1.<br />
R−N=C=O+R ′ COOH → R−NHCO−O−CO−R ′<br />
→ R−NHCO − R ′ + CO 2<br />
(1.1)<br />
These amines may act as promoters of the curing process. Moisture,<br />
which does not influence the curing reaction of the unsaturated polyester<br />
resin, would also lead to the formation of amines by the reaction of water<br />
with the isocyanate groups. 97<br />
A tricomponent interpenetrating network system consisting of castor<br />
oil-based polyurethane components, acrylonitrile, <strong>and</strong> an unsaturated<br />
polyester resin (the main component) was synthesized in order to toughen<br />
the unsaturated polyester resin. By incorporating the urethane <strong>and</strong> acrylonitrile<br />
structures, the tensile strength of the matrix (unsaturated polyester<br />
resin) decreased <strong>and</strong> flexural <strong>and</strong> impact strengths were increased. 98<br />
1.3.8.2 Epoxides<br />
Mixtures of unsaturated polyester resin systems <strong>and</strong> epoxy resins also form<br />
interpenetrating polymer networks. Since a single glass transition temperature<br />
for each interpenetrating polymer network is observed, it is suggested<br />
that both materials are compatible. On the other h<strong>and</strong>, an interlock between<br />
the two growing networks was suggested, because in the course of<br />
curing, a retarded viscosity increase was observed. 99 A network interlock
30 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
is indicated by a lower total exothermic reaction during simultaneous polymerization<br />
in comparison to the reaction of the homopolymers. 100<br />
In bismaleimide-modified unsaturated polyester–epoxy resins, the<br />
reaction between unsaturated polyester <strong>and</strong> epoxy resin could be confirmed<br />
by IR spectral studies. 101 The incorporation of bismaleimide into epoxy<br />
resin improved both mechanical strength <strong>and</strong> thermal behavior of the epoxy<br />
resin.<br />
1.3.8.3 Vinylester Resins<br />
Unsaturated polyesters modified with up to 30% of vinylester oligomer<br />
are tougheners for the unsaturated polyester matrix. The introduction of<br />
vinylester oligomer <strong>and</strong> bismaleimide into an unsaturated polyester resin<br />
improves thermomechanical properties. 102<br />
1.3.8.4 Phenolic Resins<br />
An interpenetrating network consisting of an unsaturated polyester resin<br />
<strong>and</strong> a resol-type of phenolic resin improves heat resistance but also helps<br />
to suppress the smoke, toxic gas, <strong>and</strong> heat release during combustion in<br />
comparison to a pure unsaturated polyester resin. 103<br />
1.3.8.5 Organic-inorganic Hybrids<br />
Organic-inorganic polymer hybrid materials can be prepared using an unsaturated<br />
polyester <strong>and</strong> silica gel. First an unsaturated polyester is prepared.<br />
To this polyester the silica gel precursor is added, i.e., tetramethoxysilane,<br />
methyltrimethoxysilane, or phenyltrimethoxysilane.<br />
Gelling of the alkoxysilanes was achieved at 60°C using HCl catalyst<br />
in the presence of the unsaturated polyester resin. It was confirmed by<br />
nuclear magnetic resonance spectroscopy that the polyester did hydrolyze<br />
during the acid treatment. Finally, the interpenetrating network was formed<br />
by photopolymerization of the unsaturated polyester resin. 104 It is assumed<br />
that between the phenyltrimethoxysilane <strong>and</strong> the aromatic groups in the unsaturated<br />
polyester resin π-interactions arise.<br />
1.3.9 Polyurethane Hybrid Networks<br />
The mechanical properties of the unsaturated polyester resin can be greatly<br />
improved by incorporating a polyurethane linkage into the polymer net-
Unsaturated Polyester Resins 31<br />
work. The mechanical properties also can be altered by the techniques used<br />
in segmented polyurethanes. The basic concept is to use soft segments <strong>and</strong><br />
hard segments.<br />
The polyester is prepared with an excess of diol <strong>and</strong> dilute with styrene<br />
as usual. Additional diols as chain extenders are blended into the resin<br />
solution. 4,4 ′ -Diphenylmethane diisocyanate dissolved in styrene is added<br />
to form the hybrid linkages. Suitable peroxides are added to initiate the<br />
radical curing.<br />
The curing starts with the reaction between the isocyanates <strong>and</strong> the<br />
hydroxyl groups, thus forming the polyurethane linkage. Then the crosslinking<br />
reaction takes place. 105<br />
The mechanical properties of the hybrid networks were generally<br />
improved by the incorporation of a chain extender at room temperature.<br />
Hexanediol increased the flexibility of the polymer chains, resulting in a<br />
higher deformation <strong>and</strong> impact resistance of the hybrid networks. Hybrid<br />
networks with ethylene glycol as the chain extender are stiffer.<br />
1.3.10 Flame Retardants<br />
Flame retardant compositions can be achieved by flame retardant additives,<br />
by flame retardant polyester components, <strong>and</strong> by flame retardant vinyl<br />
monomers. Halogenated compounds are still common, but there is a trend<br />
towards substituting these compounds with halogen free compositions. In<br />
halogenated systems, bromine atoms mostly are responsible for the activity<br />
of the retardant. On the other h<strong>and</strong>, a disposal problem arises when a<br />
pyrolytic recycling method is intended at the end of the service times of<br />
such articles. Flame retardants are summarized in Table 1.6.<br />
In general, bromine compounds are more effective than chlorine<br />
compounds. Suitable additives are chlorinated alkanes, brominated bisphenols<br />
<strong>and</strong> diphenyls. Antimony trioxide is synergistic to halogenated<br />
flame retardants. It acts also as a smoke suppressant in various systems. 106<br />
1.3.10.1 Flame Retardant Additives<br />
Decabromodiphenyloxide. Decabromodiphenyloxide with 2% of antimony<br />
trioxide increases the oxygen index values linearly with the bromine<br />
content. Some improvement of the mechanical properties can be achieved<br />
by adding acrylonitrile to the polyester. 107 Decabromodiphenyloxide with
32 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 1.6: Flame Retardants for Unsaturated Polyester Resins<br />
Flame Retardant<br />
Remarks Reference<br />
Aluminum hydroxide<br />
Melamine diphosphate<br />
Melamine cyanurate<br />
108<br />
Ammonium polyphosphate<br />
109<br />
Antimony trioxide<br />
Synergist<br />
Zinc hydroxystannate<br />
110–112<br />
2-Methyl-2,5-dioxo-1-oxa-2-phospholane <strong>Reactive</strong><br />
113<br />
Decabromodiphenyloxide<br />
114<br />
HET acid<br />
<strong>Reactive</strong><br />
2,6,2 ′ ,6 ′ -Tetrabromobisphenol A (TBBPA) <strong>Reactive</strong><br />
115<br />
Tetrachlorophthalic anhydride<br />
<strong>Reactive</strong><br />
Tetrabromophthalic anhydride<br />
<strong>Reactive</strong><br />
antimony trioxide increases the activation energy of the decomposition of<br />
the unsaturated polyester. 114<br />
Aluminum Hydroxide. Fillers, such as aluminum hydroxide, yield crystallization<br />
water at higher temperatures, thus achieving a certain flame retardancy.<br />
At high degrees of filling in the range of 150 to 200 parts of aluminum<br />
hydroxide per 100 parts of unsaturated polyester resin, it is possible<br />
to achieve self-extinguishing <strong>and</strong> a low smoke density. A disadvantage of<br />
such systems is that the entire material has a high density. The density can<br />
be reduced, if hollow filler is used for reinforcement. 116<br />
Lower amounts of aluminum hydroxide are sufficient, if red phosphorus<br />
<strong>and</strong> melamine or melamine cyanurate is admixed. 108 Magnesium<br />
hydroxide acts in a similar way to aluminum hydroxide.<br />
Ammonium polyphosphate. Ammonium polyphosphate is a halogenfree<br />
flame retardant for unsaturated polyester resin composites. 109 Commonly<br />
used are ammonium polyphosphates having the general formula<br />
(NH 4 ) n+2 P n O 3n+1 .<br />
A significant reduction of the flame spread index is achieved by<br />
a combination of a polyhydroxy compound, a polyphosphate, melamine,<br />
cyanuric acid, melamine salts, e.g., melamine cyanurate, <strong>and</strong> a polyacrylate<br />
monomer. 117<br />
The fire retardant polyacrylate component should be distinguished
Unsaturated Polyester Resins 33<br />
O<br />
H 3 C P CH 2<br />
O CH 2<br />
C<br />
O<br />
O<br />
O<br />
P CH 2 CH 2 C O<br />
CH 3<br />
Figure 1.9: Ring opening of 2-Methyl-2,5-dioxo-1-oxa-2-phospholane 113<br />
from the unsaturated monomers that may be included as crosslinkers in the<br />
resin systems. It cannot be ruled out that the polyacrylate may become involved<br />
in the crosslinking reactions of such systems. However, it has been<br />
observed that the fire retardant effect of the polyacrylates is also effective<br />
in those resin systems that do not involve curing by way of unsaturated<br />
groups. Preferred polyacrylates are those having backbones of a type that<br />
is known to contribute to char formation, for example, those having alkylene<br />
or oxyalkylene backbones. 118<br />
<strong>Reactive</strong> Phosphor Compound. Oxaphospholanes are heterocyclic compounds.<br />
Certain derivatives are reactive to alcohols <strong>and</strong> can be incorporated<br />
in a polyester backbone. Due to their phosphor content they also act<br />
as flame retardants, with the advantage that they are chemically bound to<br />
the backbone. 113 The ring opening reaction of 2-methyl-2,5-dioxo-1-oxa-<br />
2-phospholane is shown in Figure 1.9. As a side effect, phosphoric compounds<br />
increase the adhesion of the final products, without toughening too<br />
much.<br />
Exp<strong>and</strong>able Graphite. The flammability of crosslinked unsaturated polyester<br />
resins is reduced by the addition of exp<strong>and</strong>able graphite even at levels<br />
as low as 7 phr. Exp<strong>and</strong>able graphite is particularly useful when used in<br />
combination with ammonium polyphosphate or with a halogenated flame<br />
retardant. 119<br />
1.3.10.2 Flame Retardant Polyester Components<br />
The flame retardant can be also built in the polymer backbone. Examples<br />
are HET acid, tetrachlorophthalic anhydride, <strong>and</strong> tetrabromophthalic anhydride.<br />
The mechanical properties decrease with increasing halogen content
34 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
in the backbone. 120 HET acid is used for fireproof applications, e.g., for<br />
panels in subways, etc.<br />
1.3.10.3 Flame Retardant Vinyl Monomers<br />
Dibromostyrene is a suitable brominated vinyl monomer. 121 However, it<br />
is not commonly used. Dibromoneopentylglycol <strong>and</strong> diallyl ether of bromobutenediol<br />
have been used as curing agents for unsaturated polyester<br />
resins in paint coatings. Both monomers act effectively against inhibition<br />
by oxygen. The bromine content decreases the flammability of the final<br />
products. The monomers can be obtained in a direct allylation by the use<br />
of allyl bromide. The resins can be photocured in a system consisting of<br />
mono- or diazide <strong>and</strong> hydroxyalkylphenone. 122<br />
Flame-retardant polyester resin polymers wherein the ability of the<br />
polyester resin to transmit light is not significantly affected can be formulated<br />
using, instead of antimony trioxide, organic antimony compounds<br />
together with halogen flame retardants. Antimony ethylene glycoxide (i.e.,<br />
ethylene glycol antimonite) can be incorporated in the polyester backbone.<br />
Antimony tri-alloxide <strong>and</strong> antimony methacrylate are vinyl monomers. 123<br />
The antimony alkoxides can be prepared by dissolving antimony trichloride<br />
in a slight excess of the corresponding alcohol in an inert solvent, e.g.,<br />
carbon tetrachloride or toluene <strong>and</strong> sparging with anhydrous ammonia.<br />
The antimony acylates are prepared by mixing the stoichiometric amounts<br />
of saturated or unsaturated acid <strong>and</strong> antimony alkoxide.<br />
In addition to good light transmission, polyester resins may contain<br />
a smaller proportion of combined antimony than those produced using antimony<br />
trioxide <strong>and</strong> still retain their self-extinguishing properties. Moreover,<br />
a smaller proportion of chlorine, than for formulations using antimony trioxide,<br />
is sufficient to retain the self-extinguishing properties.<br />
1.3.11 Production Data<br />
Global production data of the most important monomers used for unsaturated<br />
polyester resins are shown in Table 1.7.<br />
1.4 CURING<br />
Curing is achieved in general with a radical initiator <strong>and</strong> a promoter. A<br />
promoter assists the decomposition of the initiator delivering radicals, even
Unsaturated Polyester Resins 35<br />
Table 1.7: Global Production/Consumption Data of Important Monomers<br />
<strong>and</strong> <strong>Polymers</strong> 124<br />
Monomer Mill. Metric tons Year Reference<br />
Methyl methacrylate 2 2002<br />
125<br />
Styrene 21 2001<br />
126<br />
Phthalic anhydride 3.2 2000<br />
127<br />
Isophthalic acid 0.270 2002<br />
128<br />
Dimethyl terephthalate (DMT)<br />
<strong>and</strong> terephthalic acid (TPA) 75 2004<br />
129<br />
Adipic Acid 2 2001<br />
130<br />
Bisphenol A 2 1999<br />
131<br />
Maleic anhydride 1.3 2001<br />
132<br />
1,4-Butanediol 1 2003<br />
133<br />
Dicyclopentadiene 0.290 2002<br />
134<br />
Unsaturated Polyester Resins 1.6 2001<br />
135<br />
at low temperatures at which the initiator alone does not decompose at a<br />
sufficient rate. Promoters are also addressed as accelerators.<br />
1.4.1 Initiator Systems<br />
Even when a wide variety of initiators are available, common peroxides<br />
are used for cold curing <strong>and</strong> hot curing. Coatings of unsaturated polyester<br />
resins are cured with light sensitive materials.<br />
Peroxide initiators include ketone peroxides, hydroperoxides, diacyl<br />
peroxides, dialkyl peroxides, alkyl peresters, <strong>and</strong> percarbonates. Azo compounds,<br />
such as 2,2 ′ -azobis(isobutyronitrile) <strong>and</strong> 2,2 ′ -azobis(2-methylbutyronitrile)<br />
are also suitable. These curing agents can be used alone, or two<br />
or more can be used in combination. Some peroxide initiators are shown<br />
in Table 1.8.<br />
1.4.1.1 In-Situ Generated Peroxides<br />
Allyl alcohol propoxylate can generate a peroxide in-situ in the presence<br />
of metal salt promoter. This peroxide cures the unsaturated polyester resin.<br />
The curing proceeds with a very low exothermic reaction <strong>and</strong> low product<br />
shrinkage. 136
36 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Peroxide Type<br />
Ketone Peroxides<br />
Hydroperoxides<br />
Diacyl peroxides<br />
Dialkyl peroxides<br />
Alkyl peresters<br />
Percarbonates<br />
Table 1.8: Peroxide Initiators<br />
Example<br />
Methylethylketone peroxide<br />
Acetylacetone peroxide<br />
Cumene hydroperoxide<br />
Dibenzoyl peroxide<br />
Dicumyl peroxide<br />
tert-Butylcumyl peroxide<br />
tert-Butylperoxy-2-ethylhexanoate<br />
tert-Butylperoxybenzoate<br />
tert-Amylperoxybenzoate<br />
tert-Hexylperoxybenzoate<br />
bis(4-tert-Butylcyclohexyl)peroxydicarbonate<br />
1.4.1.2 Functional Peroxides<br />
Peroxides can be functionalized. Functional peroxides based on pyromellitic<br />
dianhydride, poly(ethylene glycol)s <strong>and</strong> tert-butyl hydroperoxide contain<br />
two types of functional groups:<br />
1. Carboxylic groups that can participate in ionic reactions,<br />
2. Peroxide groups that can initiate certain radical reactions.<br />
The oligoesters are able to form three-dimensional networks when<br />
heated to 130 °C. 137<br />
1.4.1.3 Photoinitiators<br />
Photoinitiators are mostly used for coating applications. Some common<br />
photoinitiators are listed in Table 1.9. A common problem is yellowing<br />
during curing. α-Aminoacetophenones <strong>and</strong> thioxanthone derivatives impart<br />
yellowness. Such derivatives are used in thin layers.<br />
Although suitable initiators for clear systems have become available<br />
only in the last few years, photoinitiators for pigmented systems have been<br />
developed for some time. Problems with regard to the absorbtion of ultraviolet<br />
light, needed for curing, arise when the coating is pigmented or<br />
when it is UV stabilized for outdoor applications. Ultraviolet stabilizers<br />
consist of ultraviolet absorbers or hindered amine light stabilizers. The<br />
curing performance depends on the pigment absorption <strong>and</strong> particle size.
Photoinitiator<br />
Unsaturated Polyester Resins 37<br />
Table 1.9: Common Photoinitiators<br />
Reference<br />
Benzoin methyl ether<br />
138<br />
2,2-Dimethoxy-2-phenylacetophenone<br />
2-Hydroxy-2-methylphenylpropane-1-one<br />
α-Hydroxy-acetophenone<br />
139<br />
Bis(2,6-dimethoxybenzoyl)-2,4,4-trimethylpentylphosphine oxide<br />
140<br />
2-Hydroxy-2-methyl-1-phenyl-propan-1-one<br />
2,4,6-Trimethylbenzoyldiphenylphosphine oxide<br />
Bis(2,6-dichlorobenzoyl)-(4-propylphenyl)phosphine oxide<br />
The adsorption of bisacylphosphine oxides is in the near UV-visible<br />
range, <strong>and</strong> thus at much lower energy than other common photoinitiators.<br />
Those photoinitiators therefore allow the curing of thick pigmented layers.<br />
Acylphosphine oxides were originally used in dental applications.<br />
Acylphosphine oxides <strong>and</strong> bisacylphosphine oxides are prone to solvolysis<br />
attack; that is why the carbon phosphor bond is shielded by bulky<br />
groups.<br />
Earlier investigations on acylphosphine oxides, in particular 2,4,6-trimethylbenzoyldiphenylphosphine<br />
oxide, did not show any advantage over<br />
2,2-dimethoxy-2-phenylacetophenone. It was even concluded that acylphosphonates<br />
cannot be considered useful photoinitiators.<br />
141, 142<br />
A mixture of bis(2,6-dimethoxybenzoyl)-2,4,4-trimethylpentylphosphine<br />
oxide <strong>and</strong> 2-hydroxy-2-methyl-1-phenyl-propan-1-one is suitable for<br />
curing thick pigmented furniture coatings. 140 The structures of these compounds<br />
are shown in Figure 1.10. Further, a combination of a bis-acylphosphineoxide<br />
<strong>and</strong> an α-hydroxy-acetophenone photoinitiator overcomes the<br />
limitations imposed by filtering of UV radiation by the pigments <strong>and</strong> provides<br />
a balanced cure. 139<br />
The chloro compounds, e.g., bis(2,6-dichlorobenzoyl)-(4-propylphenyl)phosphine<br />
oxide are less satisfactory, c.f. Figure1.11.<br />
1.4.2 Promoters<br />
There is a difference between hydroperoxides such as methylethylketone<br />
peroxide <strong>and</strong> peroxides, such as dibenzoyl peroxide. Redox promoters,<br />
e.g., cobalt naphthenate, can stimulate the decomposition of hydroperoxides<br />
catalytically, whereas they cannot stimulate the decomposition of di-
38 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
OCH 3<br />
O<br />
CH 3 O<br />
O<br />
C P C<br />
OCH 3<br />
CH3 O<br />
H 3 C<br />
CH 3<br />
C CH 2<br />
CH 3<br />
CH 2<br />
CH CH 3<br />
Bis(2,6-dimethoxybenzoyl)-2,4,4-trimethylpentylphosphine<br />
O<br />
C<br />
CH 3<br />
C OH<br />
CH 3<br />
2-Hydroxy-2-methyl-1-phenyl-propan-1-one<br />
Figure 1.10: Bis(2,6-dimethoxybenzoyl)-2,4,4-trimethylpentylphosphine <strong>and</strong><br />
2-Hydroxy-2-methyl-1-phenyl-propan-1-one<br />
peroxides. Therefore, for hydroperoxides only catalytic amounts of metal<br />
salts are necessary, whereas the salts do not act readily on diperoxides. The<br />
mechanism of catalytic action of metal salts is shown in Eq. 1.2.<br />
ROOH+Co 2+ → RO ·+OH − + Co 3+<br />
ROOH+Co 3+ → ROO ·+H + + Co 2+ (1.2)<br />
The cobalt ion is either oxidized or reduced by the peroxides depending<br />
on its value. If too much promoter is added, then the exotherm<br />
can be very high. Since the thermal conductivity of polymers is small, the<br />
heat of reaction cannot be transported out of the resin. The material would<br />
overheat <strong>and</strong> gas bubbles would form.<br />
Promoters can be metal soaps, e.g., cobalt octoate or manganese octoate,<br />
or further metal chelates such as cobalt acetylacetonate <strong>and</strong> vanadium<br />
acetylacetonate. These promoters are redox promoters <strong>and</strong> amine<br />
compounds such as N,N-dimethylaniline. These accelerators can be used<br />
alone, or two or more kinds of them can be used in combination.<br />
Examples of promoters are shown in Table 1.10. The auxiliary accelerator<br />
is used for enhancing the potency of the accelerator <strong>and</strong> includes, for
Unsaturated Polyester Resins 39<br />
Cl<br />
O<br />
C<br />
P<br />
Cl<br />
O<br />
C<br />
Cl<br />
Cl<br />
H 3 C<br />
CH 2<br />
CH 2<br />
Bis(2,6-dichlorobenzoyl)-(4-propylphenyl)phosphine oxide<br />
H 3 C<br />
CH 3<br />
O<br />
CH 3<br />
C<br />
O<br />
P<br />
2,4,6-Trimethylbenzoyl-diphenylphosphine oxide<br />
Figure 1.11: 2,4,6-Trimethylbenzoyldiphenylphosphine oxide <strong>and</strong> Bis(2,6-dichlorobenzoyl)-(4-propylphenyl)phosphine<br />
oxide<br />
Table 1.10: Promoters<br />
Promoter Type Example<br />
Metal soaps Cobalt octoate<br />
Manganese octoate<br />
Metal chelates Cobalt acetylacetonate<br />
Vanadium acetylacetonate<br />
Amine compounds N,N-Dimethylaniline
40 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 1.11: Initiator Promoter Systems<br />
Initiator Promoter Temperature °C<br />
Methylethylketone peroxide Cobalt naphthenate 20<br />
Dibenzoyl peroxide N,N-Dimethylaniline 60<br />
Di-tert-butyl peroxide 130<br />
tert-Butylperoxybenzoate 130<br />
example, acetylacetone, ethyl acetoacetate <strong>and</strong> anilide acetoacetate. These<br />
auxiliary accelerators can be used alone, or two or more of them can be<br />
combined.<br />
1.4.3 Initiator Promoter Systems<br />
Some common initiator promoter systems are shown in Table 1.11. Methylpropylketone<br />
peroxide offers some advantage over methylethylketone<br />
peroxide, as the curing times are shorter. 143<br />
Diperoxyketal initiators are used for high-temperature molding processes.<br />
Dichloroacetic acid is a suitable promoter. It does not negatively<br />
influence the pot life <strong>and</strong> the cure cycle. 144<br />
1.4.4 Polymerization<br />
The initiators together with the accelerator initiate a crosslinking copolymerization.<br />
The monomer reactivity ratios for the system styrene/fumarate<br />
indicate an alternating system, i.e., a styrene radical reacts with a fumarate<br />
unit, <strong>and</strong> vice versa. On the other h<strong>and</strong>, the system styrene/maleate will<br />
tend to form blocks. Therefore, the fumarate system yields final products<br />
with better properties. Fortunately the maleate unit isomerizes during the<br />
condensation reaction.<br />
If a nonazeotropic composition is used, then the ratio of styrene to<br />
polymerizable double bonds in the polyester varies in the course of curing.<br />
Such systems show a decrease in network density in the course of<br />
conversion. 145<br />
1.4.4.1 Kinetics of Curing<br />
The kinetics of curing can be conveniently investigated by differential scanning<br />
calorimetry <strong>and</strong> infrared spectroscopy. Both methods have been com-
Unsaturated Polyester Resins 41<br />
pared. 146 The overall conversion measured by differential scanning calorimetry<br />
is in-between the styrene consumption <strong>and</strong> the consumption of the<br />
pending double bonds in the polyester obtained by infrared spectroscopy.<br />
The curing of laminates containing 50 to 70% glass fiber mat can<br />
be monitored by Raman spectroscopy. 147 Also, white <strong>and</strong> lightly colored<br />
gel coats can easily be monitored by Raman spectroscopy, but fluorescent<br />
problems are encountered with heavily colored pigments.<br />
Using differential scanning calorimetry, both isothermal runs <strong>and</strong><br />
temperature programmed runs can be used. Usually a complete conversion<br />
is not achieved during ordinary curing.<br />
There are two portions of reaction enthalpy that can be investigated<br />
under laboratory conditions,<br />
1. The enthalpy characterizing the styrene homopolymerization <strong>and</strong><br />
copolymerization during curing,<br />
2. A residual enthalpy that can be determined by heating up to near<br />
the degradation point of the resin.<br />
At isothermal curing experiments, it was found that the sum of enthalpy<br />
of polymerization <strong>and</strong> residual enthalpy depends on the curing (isothermal)<br />
temperature. 148<br />
An unsaturated polyester resin initiated with a curing system of methylethylketone<br />
peroxide <strong>and</strong> a cobalt salt as promoter was studied by dynamic<br />
scans from −100°C to 250°C at heating rates from 2°C/min to<br />
25°C/min. The amount of heat generated by a curing reaction decreases<br />
with increasing heating rate. The energy of activation of the overall reaction<br />
is around 90 kJ/mol. The traces can be fitted by either an empiric<br />
model or a model based on the theory of free-radical polymerization. 149<br />
The rate of curing depends on the amount of initiator added to the<br />
mixture. A universal isoconversional relationship of the type<br />
t = d − bln[I] 0 + E a<br />
RT<br />
(1.3)<br />
was established that expresses the dependency of the curing time t on the<br />
temperature, T, <strong>and</strong> the initial concentration of the initiator [I] 0 <strong>and</strong> the<br />
energy of activation E a . 150<br />
Gel Point. At a certain conversion the reacting mixture rather suddenly<br />
changes its appearance: it gels. The gel point is an important parameter for
42 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
the pot life time. The gel point can be determined most simply by stirring<br />
from time to time, although there are other more sophisticated methods<br />
available.<br />
A well-known phenomenon in radical polymerization is the acceleration<br />
at moderate conversion which is addressed as the Trommsdorff effect.<br />
This effect can also be observed in crosslinking polymerization. The<br />
increase in rate causes a temperature rise in the bulk material. It was found<br />
that the gel time corresponds closely to the initial rise of the temperature. 151<br />
The same is true when inhibitors are added or when the curing system<br />
is changed. For example, the addition of a tert-butyl catechol inhibitor<br />
increases the gel time in a linear fashion <strong>and</strong> the exothermic reaction is<br />
similarly delayed. An increase in the concentrations of initiator (either<br />
methylethylketone peroxide or acetyl acetone peroxide) or cobalt octoate<br />
promoter decreases the gel time.<br />
The gel point has been extrapolated by thermal mechanical analysis,<br />
as the point at which the shrinkage rate drops to zero <strong>and</strong> the dimensions<br />
of the material show no appreciable change. 152<br />
The curing characteristics can also be measured by the change of<br />
ultrasonic properties in the course of curing. 153 The sound velocity is constant<br />
until the gel point is reached. Afterwards the sound velocity increases<br />
to a plateau. Reaching the plateau indicates the end of the chemical reaction.<br />
The attenuation reaches a maximum which is attributed to the vitrification.<br />
The transition into the vitreous state causes a strong change of the<br />
acoustic properties.<br />
The glass transition temperature increases continuously with conversion.<br />
When the glass transition temperature reaches the polymerization<br />
temperature, then vitrification occurs. Vitrification strongly hinders the<br />
mobility of the reactive groups. For this reason, the polymerization reaction<br />
slows down or stops before complete conversion is reached.<br />
The increase of the longitudinal sound velocity with curing time can<br />
be associated with the increase of longitudinal modulus L ′ , while the irreversible<br />
viscous losses are responsible for the increase of sound attenuation.<br />
Kinetic Model. To describe the curing behavior of sheet molding compounds,<br />
a kinetic model based on radical polymerization mechanisms was<br />
developed. 154 In the model, three radical reaction steps are involved:
Unsaturated Polyester Resins 43<br />
Initiation : I 0 → 2R·<br />
Propagation : R ·n +M → R·n+1<br />
Inhibition : R· → Products<br />
(1.4)<br />
Here I 0 is the (initial) initiator concentration, R·n a growing radical with<br />
chain length n, <strong>and</strong> M a monomer unit. R· refers to the total concentration<br />
of growing radicals. The kinetic constants were experimentally obtained<br />
by differential scanning calorimetry (DSC) measurements in model unsaturated<br />
polyester resins.<br />
Another kinetic model has been presented that is based on the irreversible<br />
thermodynamic fluctuation theory. Because the glass transition<br />
temperature is related to molecular relaxation processes, the chemical kinetics<br />
also can be explained in terms of fluctuation theory. 155<br />
The physical or mechanical properties of polymers during curing can<br />
be expressed by Eq. 1.5<br />
P(∞) − P(t)<br />
(<br />
P(∞) − P(0) = exp −(t/τ) β) . (1.5)<br />
P(t), P(∞), <strong>and</strong> P(0) is some property at times t,∞, <strong>and</strong> 0, β is a constant,<br />
<strong>and</strong> τ is the curing relaxation time, τ ∝ exp(H/RT), where H is the activation<br />
energy of the curing reaction. If the property P is addressed as the<br />
monomer concentration, then the left h<strong>and</strong> term in Eq. 1.5 is the fraction<br />
of unreacted monomer 1 − α. Thus the conversion α is a function of the<br />
curing relaxation time, reaction time, <strong>and</strong> the reaction temperature.<br />
155, 156<br />
1.4.4.2 Phase Separation<br />
A phase separation may occur in the course of curing, when styrene is in<br />
excess. In this case a crosslinked phase <strong>and</strong> a poly(styrene) rich phase<br />
appear.<br />
In the case of unsaturated polyester systems, the phase separation<br />
occurs mainly by chemical changes of the system, in contrast to the more<br />
common thermally induced phase separation. The phase separation is<br />
therefore addressed as a chemically induced phase separation. Thermodynamic<br />
models have been established to underst<strong>and</strong> this phenomenon. 157<br />
The final morphology of the resin is primarily determined by the<br />
phase separation process <strong>and</strong> the gelation resulting from the polymerization.<br />
158 The cured polymer of a single phase resin shows a flake-like structure,<br />
while spherical particles form in the two-phase system. 159
44 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
The phase behavior can be observed by measuring the glass transition<br />
temperatures where shoulders are observed in the presence of a twophase<br />
system. The shoulders become more evident utilizing dynamic mechanical<br />
analysis by plotting logtanδ vs. temperature. 160<br />
Phase separation is an important feature in low-profile resin systems.<br />
Here the system separates in a thermoplastic-rich phase <strong>and</strong> in an unsaturated<br />
polyester-rich phase. This two-phase structure provides a weak interface<br />
where microcracking can initiate <strong>and</strong> microvoids can form to compensate<br />
the shrinkage. 90<br />
In such systems an optical microscope equipped with a heating chamber<br />
is employed to observe the phase separation process during curing. At<br />
the same time, conversion is monitored by infrared spectroscopy. The results<br />
show that the copolymerization routes locate between the azeotropic<br />
<strong>and</strong> the alternating copolymerization line, <strong>and</strong> shift gradually toward the<br />
azeotropic line.<br />
1.5 PROPERTIES<br />
1.5.1 Structure Properties Relationships<br />
The properties can be widely influenced by the choice of the components,<br />
since there is a wide variety of compounds. Some aspects are briefly indicated<br />
in Table 1.1.<br />
Aliphatic chains, both in the acid moiety <strong>and</strong> in the diol moiety,<br />
will result in comparatively soft materials. Therefore, 1,2-butanediol <strong>and</strong><br />
diethylene glycol <strong>and</strong> adipic acid will make the resin softer than phthalic<br />
anhydride. The rigidity decreases in the following order: 1,2-propanediol,<br />
2,3-butanediol, 1,4-butanediol, dipropylene glycol, diethylene glycol. For<br />
acids the rigidity decreases in the order orthophthalic acid, isophthalic acid,<br />
succinic acid, adipic acid, glutaric acid, isosebacic acid, <strong>and</strong> pimelic acid. 1<br />
More rigid materials do not absorb water as much as flexible materials.<br />
Therefore, because there is less water available, the rigid materials<br />
show better resistance to hydrolysis. Bisphenol A <strong>and</strong> neopentyl glycol-containing<br />
resins shield the access of small molecules to the ester group<br />
<strong>and</strong> therefore they exhibit a better chemical resistance.<br />
The crosslink density grows with the amount of maleic anhydride<br />
feed. The rigidity can be controlled with the content of maleic anhydride<br />
in the polyester. The glass transition temperature also increases with increasing<br />
crosslinking density.
Unsaturated Polyester Resins 45<br />
The resistance against hydrolysis increases, as the ester linkages are<br />
more stable. Bulky alcohol molecules, like neopentyl glycol, cyclohexanediol,<br />
or hydrogenated bisphenol A, are used for hydrolytic resistant materials.<br />
The alcohols are used in combination with isophthalic acid <strong>and</strong><br />
terephthalic acid.<br />
1.5.2 Hydrolytic Stability<br />
The ester group is a weak link with regards to hydrolysis. Hydrolysis occurs<br />
in aqueous media <strong>and</strong> is enhanced at elevated temperatures <strong>and</strong> in<br />
particular in alkaline media.<br />
The long-term behavior of glass fiber-reinforced plastic pipes was<br />
tested in an aqueous environment at 20°C. The strength of the wet pipes<br />
after a 1000 hour loading reduced to about 60% of the dry strength in<br />
short-term loading. 161<br />
1.5.3 Recycling<br />
1.5.3.1 Poly(ethylene terephthalate) Waste Products<br />
Oligomers obtained from depolymerization of poly(ethylene terephthalate)<br />
waste products can be reused. The glycolysis products can be used for the<br />
synthesis of polyester polyols for rigid polyurethane foams <strong>and</strong> also for<br />
the synthesis of unsaturated maleic or fumaric polyester resins. Bis(2-hydroxyethyl)terephthalate<br />
(BHET) is the main product from the glycolysis<br />
of poly(ethylene terephthalate). A mixture of maleic anhydride <strong>and</strong> sebacic<br />
acid is added <strong>and</strong> a condensation is performed. 162<br />
The glycolysis reaction is conducted by heating poly(ethylene terephthalate)<br />
<strong>and</strong> the glycol in a nitrogen atmosphere at a temperature preferably<br />
within a range from 200°C to 260°C to obtain a terephthalate oligomer<br />
48 containing two to three terephthalate units. Zinc acetate is a suitable<br />
transesterification catalyst. 163<br />
Unsaturated polyesters based on the glycolyzed poly(ethylene terephthalate)with<br />
propylene glycol or diethylene glycol <strong>and</strong> mixtures of both<br />
glycols show a broad bimodal molecular weight distribution. Larger molecular<br />
weight oligomers were obtained with increasing diethylene glycol<br />
contents in the glycol mixtures. The tensile modulus decreased <strong>and</strong> the<br />
toughness of cured products increased with increasing diethylene glycol<br />
content. 164
46 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
A study of the glycolysis of waste bottles made from poly(ethyleneterephthalate)<br />
<strong>and</strong> back condensation with maleic anhydride indicated that<br />
the type of glycol used in glycolysis had a significant effect on the characteristics<br />
of the uncured <strong>and</strong> cured resins. 165<br />
On the other h<strong>and</strong>, it was also found that no separation of the type of<br />
bottles was needed before glycolysis, since the resins prepared from either<br />
water bottles, soft drink bottles, or a mixture of both bottles showed all<br />
the same characteristics. The properties of materials recycled in this way<br />
have been presented in detail. 166 Similarly, residues from the manufacture<br />
of dimethyl terephthalate has been tried as feedstock for the aromatic<br />
acid component <strong>and</strong> condensed with maleic anhydride. 167 The complete<br />
process of how to come from a poly(ethylene terephthalate) to a suitable<br />
unsaturated polyester resin composition is described in detail in the literature.<br />
168 The glycolysis products can be directly incorporated in an unsaturated<br />
polyester resin composition. However, toluene diisocyanate as an<br />
intermediating agent must be added. The isocyanate accelerates the curing<br />
significantly. 169 It is proposed that at the beginning of the curing, the<br />
isocyanate reacts with the oligo glycols to form chain-extended products.<br />
The glycolysis product acts as a modifier that improves the mechanical<br />
properties of the resulting composites. The procedure allows an effective<br />
utilization of the waste products. It is reasonable to use only partly<br />
glycolyzed products, when the molecular mass of the degradation products<br />
is still higher.<br />
1.5.3.2 Cured Unsaturated Polyester Resin Waste<br />
Cured unsaturated polyester resin waste can be decomposed with a decomposition<br />
component such as a dicarboxylic acid or a diamine to obtain resin<br />
raw material. The unsaturated polyester resin is re-synthesized with this resin<br />
raw material. 170 It is also possible to synthesize polyurethane resin by<br />
reacting the glycolic raw material with a diisocyanate compound. 171<br />
1.6 APPLICATIONS AND USES<br />
The properties can be adjusted in a wide range, since a wide variety of<br />
basic materials can be used. Consequently, unsaturated polyesters have a<br />
very wide area of application. They can be used either as pure resin or with
Unsaturated Polyester Resins 47<br />
fillers, or reinforced, respectively.<br />
One of the early uses of unsaturated polyesters was to produce cast<br />
items such as knife <strong>and</strong> umbrella h<strong>and</strong>les, encapsulation of decorative articles,<br />
<strong>and</strong> electronic assemblies.<br />
1.6.1 Decorative Specimens<br />
Pure resins can be used for embedding of decorative specimens. Together<br />
with a photosensitive curing formulation, furniture coatings are on the market.<br />
The most important casting application is the manufacture of buttons.<br />
1.6.2 Polyester Concrete<br />
Polymer concrete is usually composed of silica s<strong>and</strong> <strong>and</strong> a binder consisting<br />
of a thermoset resin, such as unsaturated polyester. Polyester concrete<br />
is more resistant to chemicals than conventional concrete. An unsaturated<br />
polyester concrete is developed by adding the methyl methacrylate monomer<br />
to the resin to improve the early-age strength <strong>and</strong> the workability of<br />
the UP polymer concrete. 172 The study revealed that the workability is remarkably<br />
improved as the methyl methacrylate content is increased. The<br />
ratio of filler to binder is an important parameter for the workability.<br />
1.6.3 Reinforced Materials<br />
Bulk <strong>and</strong> sheet molding compounds are used in a wide variety of areas<br />
such as transportation, electrical applications, building, <strong>and</strong> construction.<br />
Reinforced unsaturated polyester resins are used for the manufacture<br />
of articles for sanitary furniture, panels, pipes, boats, etc.<br />
There are several techniques for manufacturing the final products,<br />
i.e.,<br />
• H<strong>and</strong> lay-up process<br />
• Fiber spray-up process<br />
• Cold press molding, hot press molding<br />
• Sheet molding, bulk molding<br />
• Wet-mat molding<br />
• Pultrusion<br />
In the h<strong>and</strong> lay-up process, parts in an open, glass reinforced, mold<br />
are produced. First the mold surface is treated with release wax <strong>and</strong> then
48 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
coated with a special polyester resin, the so-called gel coat. Then glass<br />
fibers are placed into the mold <strong>and</strong> impregnated with the formulated resin<br />
which cures after a short time. This procedure is repeated several times,<br />
until the desired thickness is reached. Finally a top coat is placed. In this<br />
way, for example, glass fiber reinforced boats can be fabricated.<br />
The fiber spray-up process is an improvement of the h<strong>and</strong> lay-up<br />
process. A spray system is used to apply both chopped glass str<strong>and</strong>s <strong>and</strong><br />
the polyester resin. The spray system places simultaneously resin, catalyst,<br />
<strong>and</strong> glass str<strong>and</strong>s by means of air pressure. The fiber spray-up process is<br />
much faster than h<strong>and</strong> lay-up process <strong>and</strong> can be automated.<br />
In cold press molding <strong>and</strong> hot press molding, a preimpregnated fiber<br />
is placed in presses <strong>and</strong> cured there.<br />
In sheet molding <strong>and</strong> bulk molding, the resin is mixed with the reinforcing<br />
material, either in bulk form or as mats or sheets. To the resin<br />
a thickener is added. The articles are formed in presses. The situation is<br />
similar in wet-mat molding.<br />
In pultrusion, the reinforcement fiber is wheeled off a spool, dipped<br />
into a resin mixture, <strong>and</strong> pulled through a heated die to cure the compound.<br />
1.6.4 Coatings<br />
Unsaturated polyester resins are used for a wide variety of coatings. The<br />
formulations are usually thixotropic. Curing is mostly achieved by UVsensitive<br />
initiators.<br />
1.6.4.1 Powder Coatings<br />
Thermosetting powder coatings have gained considerable popularity over<br />
liquid coatings for a number of reasons. Powder coatings are virtually free<br />
of harmful fugitive organic solvents normally present in liquid coatings.<br />
They give off little, if any, volatiles to the environment when cured. This<br />
eliminates solvent emission problems <strong>and</strong> exposure risk of workers employed<br />
in the coating operations.<br />
Powder coatings also improve working hygiene, since they are in<br />
dry solid form with no messy liquids associated with them to adhere to the<br />
clothes of the workers <strong>and</strong> the coating equipment. Furthermore, they are<br />
easily swept up in the event of a spill without requiring special cleaning<br />
<strong>and</strong> spill containment supplies.
Unsaturated Polyester Resins 49<br />
Table 1.12: Special <strong>Applications</strong> of Polyester Resins<br />
Application<br />
Reference<br />
Polyester concrete<br />
173<br />
Bone cement<br />
174<br />
Coatings<br />
Road paints<br />
175<br />
Electronic <strong>and</strong> microwave industries<br />
121<br />
Electrically conductive resins<br />
176<br />
Toner material<br />
177<br />
Compatibilizers<br />
178<br />
Pour point depressants<br />
179<br />
<strong>Reactive</strong> melt modifier<br />
180<br />
Another advantage is that they are 100% recyclable. Over sprayed<br />
powders are normally recycled during the coating operation <strong>and</strong> recombined<br />
with the original powder feed. This leads to very high coating efficiencies<br />
<strong>and</strong> minimal waste generation.<br />
However, in spite of the many advantages, powder coatings traditionally<br />
have not been suitable for heat sensitive substrates, such as wood<br />
<strong>and</strong> plastic articles, due to the high temperatures dem<strong>and</strong>ed to fuse <strong>and</strong><br />
cure the powders.<br />
Unsaturated polyester powder coatings are available that undergo<br />
rapid polymerization at low temperatures, making them particularly attractive<br />
for coating of heat sensitive substrates.<br />
Low temperature curable unsaturated polyester powder coatings contain<br />
polyols with active hydrogens. Allylic, benzylic, cyclohexyl, <strong>and</strong> tertiary<br />
alkyl hydrogen atoms are readily abstracted during free radical induced<br />
curing to form the corresponding stable allylic, benzylic, cyclohexyl,<br />
<strong>and</strong> tertiary alkyl free radicals, all of which promote curing at the surface<br />
of the coating film in an open air atmosphere. A suitable polyol is<br />
1,4-cyclohexanedimethanol. 181<br />
1.7 SPECIAL FORMULATIONS<br />
Unsaturated polyester resins have a broad field of application. Unsaturated<br />
polyester resins for special purposes are summarized in Table 1.12.
50 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
1.7.1 Electrically Conductive Resins<br />
Electrically conductive resins can be formulated by the addition of carbon<br />
black particles. The particles have a strong tendency to agglomerate in<br />
a low-viscosity resin. The agglomeration process generates electrically<br />
conductive paths already in the uncured state.<br />
The fully cured resins containing carbon black above percolation<br />
concentration have a constant, temperature-independent conductivity, over<br />
a wide temperature range. 176<br />
1.7.2 Poly(ε-caprolactone)-perfluoropolyether Copolymers<br />
Basically, fluorinated materials are attractive modifying agents because of<br />
their unique properties such as chemical inertness, solvent <strong>and</strong> high temperature<br />
resistance, barrier properties, low friction coefficient <strong>and</strong> low surface<br />
tension. These properties can be imparted to other polymeric materials<br />
by blending or copolymerization.<br />
This type of modification has been usually achieved by the use of<br />
fluorine-containing comonomers of low molecular weight which usually<br />
lead to homogeneous UP resin <strong>and</strong> therefore have to be added in significant<br />
amounts to achieve an appreciable performance improvement. Furthermore,<br />
the high cost of fluorinated monomers leads to very expensive<br />
polymeric materials.<br />
Unsaturated polyester resins can be modified by hydroxy-terminated<br />
telechelic ∗ perfluoropolyethers as comonomers during the synthesis of the<br />
polyester. 182 A disadvantage of this approach is the reactivity of these<br />
materials. A fraction of perfluoropolyether does not react.<br />
Another method of introducing fluorine into the unsaturated polyester<br />
resins is simply blending fluorinated materials. A problem arises,<br />
however, because fluorinated polymers are usually immiscible with nonfluorinated<br />
polymers. They segregate in a separate phase with poor adhesion<br />
to the non-fluorinated matrix, leading to poor mechanical properties.<br />
However, separate block or graft copolymers containing fluorinated segments<br />
can be prepared that are compatible with the unsaturated polyester<br />
resin.<br />
Poly(ε-caprolactone)-perfluoropolyether block copolymers are prepared<br />
by ring opening polymerization of ε-caprolactone with fluorinated<br />
∗ from τέλoς: end <strong>and</strong> χηλή: claw of a crab, an oligomer or polymer with well defined<br />
end groups, often star branched, whereas τ ˜ηλη means far, therefore better telochelic
Unsaturated Polyester Resins 51<br />
hydroxy ethers of the formula 1.6. Titanium tetrabutoxide is used as catalyst.<br />
183 H−(OC 2 H 4 ) n −OCH 2 CF 2 O−(C 2 F 4 O) p ×<br />
(CF 2 O) q −CF 2 CH 2 O−(C 2 H 4 O) n −H<br />
(1.6)<br />
This polymer can be added to an ordinary unsaturated polyester resin <strong>and</strong><br />
cured with conventional initiator systems.<br />
<strong>Applications</strong> of fluorine-modified unsaturated polyester resins include<br />
thermosetting resins for gel coating with excellent resistance to corrosion,<br />
water <strong>and</strong> atmospheric agents, formulations for resins <strong>and</strong> foams,<br />
etc.<br />
1.7.3 Toner Compositions<br />
Toner resins, <strong>and</strong> consequently toners are propoxylated bisphenol A fumarate<br />
resins that are crosslinked in a reactive extrusion process in the presence<br />
of the liquid 1,1-bis(tert-butylperoxy)-3,3,5-trimethylcyclohexane as<br />
initiator. 177<br />
1,1-Di(tert-butylperoxy)-3,3,5-trimethylcyclohexane has advantages<br />
in comparison to the conventionally used dibenzoyl peroxide. Dibenzoyl<br />
peroxide generates benzoic acid as a by-product, which is undesirable.<br />
Benzoic acid is difficult to remove from the crosslinked resin in that it<br />
condenses in a vacuum system, rapidly clogging the system <strong>and</strong> requiring<br />
frequent apparatus shutdowns for cleaning. As a result of the difficulty<br />
in the removal of the benzoic acid by-product, the crosslinked toner resin<br />
contains a significant amount of acids. Such acidity has been found to negatively<br />
affect the charging, the humidity sensitivity of the charging, <strong>and</strong> the<br />
background density properties of the toners.<br />
Crosslinked resins are used in making toner. The resins can be subsequently<br />
melt blended or otherwise mixed with a colorant, charge carrier<br />
additives, surfactants, emulsifiers, pigment dispersants, flow additives, etc.<br />
The resultant product can then be pulverized to form toner particles.<br />
UV curable resins for incorporation in toner particles are powders<br />
based on unsaturated polyesters <strong>and</strong> polyurethaneacrylates with bis-ethoxylated<br />
2,2-bis(4-hydroxyphenyl)propane or bis-propoxylated 2,2-bis(4-hydroxyphenyl)propane.<br />
184<br />
The toner particles can be prepared by melt kneading the toner ingredients,<br />
i.e., toner resin composition, charge control agent, pigment, etc.
52 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
After the melt kneading the mixture is cooled <strong>and</strong> the solidified mass is<br />
pulverized.<br />
1.7.4 Pour Point Depressants<br />
Copolymers of dialkyl fumarates <strong>and</strong> dialkyl maleates with vinyl acetate<br />
<strong>and</strong> vinylpyrrolidone are effective as flow improvers <strong>and</strong> pour point depressants,<br />
respectively. Among a series of similar polymers, copolymers<br />
based on didodecyl fumarate vinyl acetate are the most effective pour point<br />
depressants. 179 These polymers are suitable additives for improving the<br />
flow properties <strong>and</strong> viscosity index of lubricating oils.<br />
1.7.5 Biodegradable Polyesters<br />
Aliphatic polyesters are almost the only promising structural materials for<br />
biodegradable plastics. In fact, aliphatic unsaturated polyesters, succinic<br />
fumaric units, <strong>and</strong> 1,4-butanediol are biodegradable as such.<br />
However, the condensation of aliphatic polyesters derived from diacids<br />
<strong>and</strong> diols failed to obtain high-molecular weight polyesters. Effective<br />
transesterification catalysts, high vacuum technique <strong>and</strong> chain extenders<br />
enable the synthesis of high-molecular weight polyesters with improved<br />
mechanical properties. 185<br />
1.7.6 Bone Cement<br />
An unsaturated polyester, made from propylene glycol <strong>and</strong> fumaric acid, is<br />
suitable as resorbable bone cement. Depending on the molecular weight,<br />
poly(propylene) fumarate is a viscous liquid. A filler of calcium gluconate/hydroxyapatite<br />
is used. An injectable form of a resorbable bone<br />
cement can be crosslinked in-situ. The material cures to a hard cement<br />
degradable by hydrolysis. 186 Bis(2,4,6-trimethylbenzoyl)phenylphosphine<br />
oxide has been found useful as photoinitiator for poly(propylene) fumarate,<br />
for the treatment of large bone defects. 187<br />
Citric acid <strong>and</strong> sodium bicarbonate as the foaming agent develop<br />
porosity in the material by generating carbon dioxide during the effervescence<br />
reaction. 174
Unsaturated Polyester Resins 53<br />
1.7.7 Compatibilizers<br />
An unsaturated polyester is a suitable compatibilizer for styrene-butadiene<br />
<strong>and</strong> acrylonitrile-butadiene (NBR) rubber blends. By the addition of 10<br />
parts unsaturated polyester per hundred parts of rubber, the degree of compatibility<br />
was greatly enhanced. The rheological <strong>and</strong> mechanical properties<br />
of the blends were also improved. 178<br />
1.7.8 <strong>Reactive</strong> Melt Modification of Poly(propylene)<br />
Melt blending of poly(propylene) with a low molecular weight unsaturated<br />
polyester in the presence of peroxide in a batch mixer <strong>and</strong> a twin-screw<br />
extruder improves the morphology. Under these conditions competitive<br />
degradation <strong>and</strong> crosslinking reactions take place. These reactions result<br />
in a significant change in the viscosity ratio.<br />
Rheological studies show that depending on the process conditions<br />
some reacted PP/UP blends have a pronounced suspension behavior due<br />
to the presence of the dispersed polyester gel particles in a low molecular<br />
weight poly(propylene) matrix.<br />
Infrared studies of the blends suggest the presence of block or graft<br />
structures that promote the compatibility in the treated blends. Such blends<br />
are suitable as compatibilizers for blends of poly(propylene) with high<br />
molecular weight thermoplastic polyester blends. 180<br />
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free radicals <strong>and</strong> empirical models. Thermochim. Acta, 306(1-2):115–126,<br />
November 1997.<br />
150. X. Ramis <strong>and</strong> J. M. Salla. Effect of the initiator content <strong>and</strong> temperature on<br />
the curing of an unsaturated polyester resin. J. Polym. Sci., Part. B: Polym.<br />
Phys., 37(8):751–768, April 1999.<br />
151. W. D. Cook, M. Lau, M. Mehrabi, K. Dean, <strong>and</strong> M. Zipper. Control of gel<br />
time <strong>and</strong> exotherm behaviour during cure of unsaturated polyester resins.<br />
Polym. Int., 50(1):129–134, January 2001.<br />
152. X. Ramis, A. Cadenato, J. M. Morancho, <strong>and</strong> J. M. Salla. Curing of a thermosetting<br />
powder coating by means of DMTA, TMA <strong>and</strong> DSC. Polymer,<br />
44(7):2067–2079, March 2003.
Unsaturated Polyester Resins 65<br />
153. F. Lionetto, R. Rizzo, V. A. M. Luprano, <strong>and</strong> A. Maffezzoli. Phase transformations<br />
during the cure of unsaturated polyester resins. Mater. Sci. Eng., A,<br />
370(1-2):284–287, April 2004.<br />
154. V. Massardier-Nageotte, F. Cara, A. Maazouz, <strong>and</strong> G. Seytre. Prediction of<br />
the curing behavior for unsaturated polyester-styrene systems used for monitoring<br />
sheet moulding compounds (SMC) process. Composites Science <strong>and</strong><br />
Technology, 64(12):1855–1862, September 2004.<br />
155. H. S.-Y. Hsich. Kinetic model of cure reaction <strong>and</strong> filler effect. J. Appl.<br />
Polym. Sci., 27(9):3265–3277, September 1982.<br />
156. P. Li, X. P. Yang, Y. H. Yu, <strong>and</strong> D. S. Yu. Cure kinetics, microheterogeneity,<br />
<strong>and</strong> mechanical properties of the high-temperature cure of vinyl ester resins.<br />
J. Appl. Polym. Sci., 92(2):1124–1133, April 2004.<br />
157. R. Mezzenga, B. Pettersson, <strong>and</strong> J. A. E. Manson. Thermodynamic evolution<br />
of unsaturated polyester-styrene-hyperbranched polymers. Polym.<br />
Bull., 46(5):419–426, June 2001.<br />
158. W. Li <strong>and</strong> L. J. Lee. Low temperature cure of unsaturated polyester resins<br />
with thermoplastic additives II. structure formation <strong>and</strong> shrinkage control<br />
mechanism. Polymer, 41(2):697–710, January 2000.<br />
159. C. P. Hsu <strong>and</strong> L. J. Lee. Structure formation during the copolymerization of<br />
styrene <strong>and</strong> unsaturated polyester resin. Polymer, 32(12):2263–2271, 1991.<br />
160. E. M. S. Sanchez, C. A. C. Zavaglia, <strong>and</strong> M. I. Felisberti. Unsaturated<br />
polyester resins: influence of the styrene concentration on the miscibility<br />
<strong>and</strong> mechanical properties. Polymer, 41(2):765–769, January 2000.<br />
161. M. Farshad <strong>and</strong> A. Necola. Effect of aqueous environment on the long-term<br />
behavior of glass fiber-reinforced plastic pipes. Polymer Testing, 23(2):<br />
163–167, April 2004.<br />
162. M. E. Tawfik. Preparation <strong>and</strong> characterization of water-extended polyester<br />
based on recycled poly(ethylene terephthalate). J. Appl. Polym. Sci., 89(13):<br />
3693–3699, September 2003.<br />
163. S. H. Mansour <strong>and</strong> N. E. Ikladious. Depolymerization of poly(ethylene terephthalate)<br />
waste using 1,4-butanediol <strong>and</strong> triethylene glycol. J. Elastomer<br />
Plast., 35(2):133–148, April 2003.<br />
164. D. J. Suh, O. O. Park, <strong>and</strong> K. H. Yoon. The properties of unsaturated polyester<br />
based on the glycolyzed poly(ethylene terephthalate) with various glycol<br />
compositions. Polymer, 41(2):461–466, January 2000.<br />
165. V. Pimpan, R. Sirisook, <strong>and</strong> S. Chuayjuljit. Synthesis of unsaturated polyester<br />
resin from postconsumer PET bottles: Effect of type of glycol on characteristics<br />
of unsaturated polyester resin. J. Appl. Polym. Sci., 88(3):788–792,<br />
April 2003.<br />
166. A. Viksne, M. Kalnins, L. Rence, <strong>and</strong> R. Berzina. Unsaturated polyester<br />
resins based on PET waste products from glycolysis by ethylene, propylene,<br />
<strong>and</strong> diethylene glycols <strong>and</strong> their mixtures. Arab. J. Sci. Eng., 27(1C):33–42,<br />
June 2002.
66 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
167. B. Gawdzik, T. Matynia, <strong>and</strong> E. Zarebska. Synthesis of unsaturated polyester<br />
resins based on dimethyl terephthalate process residue. Przem. Chem.,<br />
81(8):525–527, August 2002.<br />
168. T. Yasumura <strong>and</strong> C. Yoshioka. Process for producing unsaturated polyester<br />
<strong>and</strong> unsaturated polyester resin composition. US Patent 6 353 036, assigned<br />
to Dainippon Ink <strong>and</strong> Chemicals, Inc. (Tokyo, JP), March 17 2002.<br />
169. P. Radenkov, M. Radenkov, G. Grancharov, <strong>and</strong> K. Troev. Direct usage<br />
of products of poly(ethylene terephthalate) glycolysis for manufacturing of<br />
glass fibre reinforced plastics. Eur. Polym. J., 39(6):1223–1228, June 2003.<br />
170. S. Kubota, O. Ito, <strong>and</strong> H. Miyamoto. Method of recycling cured unsaturated<br />
polyester resin waste. US Patent 5 776 989, assigned to Wakayama<br />
Prefecture (Wakayama, JP); Miyaso Chemical Co. (Wakayama, JP), July 7<br />
1998.<br />
171. S. Kubota, O. Ito, <strong>and</strong> H. Miyamoto. Method of recycling unsaturated polyester<br />
resin waste <strong>and</strong> recycling apparatus. US Patent 5 620 665, assigned to<br />
Miyaso Chemical Co. (Wakayama, JP), April 15 1997.<br />
172. K. S. Yeon, N. J. Jin, Y. H. Kwon, <strong>and</strong> K. W. Ryu. Workability <strong>and</strong> strength<br />
properties of MMA-modified UP polymer concrete. J. Polym. Eng., 23(5):<br />
385–398, September–October 2003.<br />
173. R. E. Hefner, Jr. Polymer modified unsaturated polyester for polyesteramide<br />
resin polymer concrete. US Patent 4 777 208, assigned to The Dow<br />
Chemical Company (Midl<strong>and</strong>, MI), October 11 1988.<br />
174. K. U. Lew<strong>and</strong>rowski, D. D. Hile, B. M. J. Thompson, D. L. Wise, W. W.<br />
Tomford, <strong>and</strong> D. J. Trantolo. Quantitative measures of osteoinductivity of<br />
a porous poly(propylene fumarate) bone graft extender. Tissue Eng., 9(1):<br />
85–93, February 2003.<br />
175. E. Blot <strong>and</strong> C. Stock. Road paint compositions containing an unsaturated<br />
polyester resin. US Patent 5 907 003, assigned to Lafarge Materiaux De<br />
Specialites (FR), May 25 1999.<br />
176. M. Narkis, I. Rafail, G. Victor, A. Tzur, R. Tchoudakov, <strong>and</strong> A. Siegmann.<br />
Electrically conductive thermosetting resins containing low concentrations<br />
of carbon black. J. Appl. Polym. Sci., 76(7):1165–1170, May 2000.<br />
177. J. L. Leonardo, Y. Lipovetskaya, S.-R. Nilmarie, H. Chang, D. Li, K. B.<br />
Sheth, D. A. Harrington, J. J. Ianni, P. L. Jacobs, J. S. Kittelberger, L. J.<br />
Kurtic, Jr., R. E. Lutz, D. J. O’ Keefe, <strong>and</strong> E. F. Young. Cross-linked polyester<br />
toners <strong>and</strong> process of making such toners. US Patent 6 359 105, assigned<br />
to Xerox Corp, March 19 2002.<br />
178. S. H. Mansour, S. Y. Tawfik, <strong>and</strong> M. H. Youssef. Unsaturated polyester as<br />
compatibilizer for styrene-butadiene (SBR)/acrylonitrile-butadiene (NBR)<br />
rubber blends. J. Appl. Polym. Sci., 83(11):2314–2321, March 2002.<br />
179. A. A. A. Abdel-Azim <strong>and</strong> R. M. Abdel-Aziem. Polymeric additives for<br />
improving the flow properties <strong>and</strong> viscosity index of lubricating oils. J.<br />
Polym. Res.-Taiwan, 8(2):111–118, June 2001.
Unsaturated Polyester Resins 67<br />
180. C. Wan, S. H. Patel, <strong>and</strong> M. Xanthos. <strong>Reactive</strong> melt modification of<br />
polypropylene with a crosslinkable polyester. Polym. Eng. Sci., 43(6):<br />
1276–1288, June 2003.<br />
181. J. Muthiah, J. J. Kozlowski, N. B. Shah, P. H. Radcliffe, <strong>and</strong> E. G. Nicholl.<br />
Unsaturated polyester powder coatings with improved surface cure. US<br />
Patent 6 048 949, assigned to Morton International, Inc. (Chicago, IL), April<br />
11 2000.<br />
182. F. Pilati, M. Toselli, M. Messori, U. Credali, C. Tonelli, <strong>and</strong> C. Berti. Unsaturated<br />
polyester resins modified with perfluoropolyethers. J. Appl. Polym.<br />
Sci., 67(10):1679–1691, March 1998.<br />
183. M. Messori, M. Toselli, F. Pilati, <strong>and</strong> C. Tonelli. Unsaturated polyester resins<br />
modified with poly(ε-caprolactone)-perfluoropolyethers block copolymers.<br />
Polymer, 42(25):9877–9885, December 2001.<br />
184. S. Tavernier, S. De Meutter, <strong>and</strong> D. van Wunsel. Radiation curable toner<br />
particles. EP Patent 0 821 281, assigned to Agfa Gevaert NV, January 28<br />
1998.<br />
185. M. S. Nikolic, D. Poleti, <strong>and</strong> J. Djonlagic. Synthesis <strong>and</strong> characterization of<br />
biodegradable poly(butylene succinate-co-butylene fumarate)s. Eur. Polym.<br />
J., 39(11):2183–2192, November 2003.<br />
186. K. U. Lew<strong>and</strong>rowski, J. D. Gresser, D. L. Wise, R. L. White, <strong>and</strong> D. J.<br />
Trantolo. Osteoconductivity of an injectable <strong>and</strong> bioresorbable poly(propylene<br />
glycol-co-fumaric acid) bone cement. Biomaterials, 21(3):293–298,<br />
February 2000.<br />
187. J. P. Fisher, D. Dean, <strong>and</strong> A. G. Mikos. Photocrosslinking characteristics<br />
<strong>and</strong> mechanical properties of diethyl fumarate/poly(propylene fumarate)<br />
biomaterials. Biomaterials, 23(22):4333–4343, November 2002.
68 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong>
2<br />
Polyurethanes<br />
Polyurethanes consist basically of two components, an isocyanate component<br />
<strong>and</strong> a diol component. The diol component can be a polyether endcapped<br />
diol or a polyester end-capped diol. The urethane structure may be<br />
identified as the esters of carbamic acid or ester amides of a carbonic acid.<br />
The urethane formation is achieved by the addition of a tertiary amine <strong>and</strong><br />
an organometallic compound.<br />
There are many monographs on the topic, 1–11 the most recent of<br />
W. Dias Vilar 12 <strong>and</strong> Klempner. 13 Polyurethanes also find use in medical<br />
applications.<br />
14, 15<br />
They are used to a large extent as adhesives 16 <strong>and</strong> as<br />
coatings.<br />
2.1 HISTORY<br />
Polyurethane was first described by Bayer ∗ in 1937. 17 The first polyurea<br />
was composed from hexane-1,6-diamine <strong>and</strong> hexane-1,6-diisocyanate.<br />
Two diisocyanates used at that time, diphenylmethane-4,4 ′ -diisocyanate<br />
<strong>and</strong> naphthalene-1,5-diisocyanate, are still key products in polyurethane<br />
chemistry. Besides O. Bayer, H. Rinke, A. Hoechtlen, P. Hoppe <strong>and</strong><br />
E. Meinbrenner contributed significantly to the development of polyurethanes.<br />
In 1940, toluene diisocyanate was introduced. From the beginning<br />
polyurethanes were utilized as foams, coatings, <strong>and</strong> cast elastomers.<br />
∗ Otto Bayer, born in Frankfurt/Main 1902, died 1982<br />
69
70 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Cl<br />
R NH 2<br />
+ C<br />
Cl<br />
O R N C O<br />
Figure 2.1: Synthesis of Isocyanates<br />
2.2 MONOMERS<br />
Monomers for the synthesis of polyurethanes consist of two types, i.e.,<br />
diisocyanates <strong>and</strong> polyols.<br />
2.2.1 Diisocyanates<br />
The basic synthesis of isocyanates is shown in Figure 2.1. The synthesis<br />
starts with an amine, aliphatic or aromatic <strong>and</strong> phosgene. The isocyanate<br />
is formed by the elimination of two molecules of HCl.<br />
Phosgene Route. The synthesis route via phosgene was invented in 1884<br />
by Hentschel, although isocyanates had been discovered in 1848 by Wurtz.<br />
The synthesis runs via two basic steps, i.e.<br />
1. Formation of the carbamic chloride,<br />
2. Elimination of hydrochloric acid.<br />
The industrial synthesis has to minimize the various side reactions<br />
that may occur, as shown in Figure 2.2.<br />
Phosgene-free Route. There is also a phosgene-free synthesis route,<br />
because of the hazards of h<strong>and</strong>ling phosgene. The route is shown in Figure<br />
2.3. The synthesis starts with nitrobenzene; from that the ethyl urethane<br />
is directly formed with carbon monoxide <strong>and</strong> ethanol. The urethane is<br />
dimerized by a carbonylation reaction. Finally, by heating the urethane is<br />
decomposed into the isocyanate <strong>and</strong> the alcohol.<br />
Typical diisocyanates are shown in Table 2.1. Aromatic diisocyanates<br />
are shown in Figure 2.4. The highly volatile isocyanates are very toxic.<br />
During curing there is also an emission of the unreacted isocyanate.<br />
The emission also depends on the reactivity of the particular isocyanate, as
Polyurethanes 71<br />
R NH 2 + HCl R NH 3 Cl<br />
R N C O<br />
+<br />
H<br />
N R<br />
H<br />
H<br />
H<br />
R<br />
N<br />
C<br />
N<br />
R<br />
O<br />
R NH 2<br />
R NH 2<br />
+<br />
Cl<br />
Cl<br />
C<br />
R<br />
H N<br />
O C O<br />
H N<br />
R<br />
Figure 2.2: Side Reactions in Isocyanate Synthesis: Salt Formation with HCl<br />
generated, Formation of Urea from Amine <strong>and</strong> Isocyanate, Formation of Urea<br />
from Amine <strong>and</strong> Phosgene<br />
CO +<br />
NO 2<br />
CH 3<br />
CH 2 OH<br />
NH C<br />
O CH 2<br />
CH 3<br />
O<br />
CHO<br />
CH 3<br />
CH 3<br />
CH 2<br />
CH 2<br />
O<br />
O<br />
C HN<br />
CH2<br />
NH C<br />
O<br />
O<br />
OCN<br />
CH 2<br />
NCO<br />
Figure 2.3: Phosgene-free Synthesis of Diisocyanates
72 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
CH 3<br />
NCO<br />
OCN<br />
CH 3<br />
NCO<br />
NCO<br />
Toluene 2,4-diisocyanate<br />
Toluene 2,6-diisocyanate<br />
OCN<br />
CH 2<br />
NCO<br />
4,4'-Diphenyl methane diisocyanate<br />
NCO<br />
CH 2<br />
NCO<br />
2,4'-Diphenyl methane diisocyanate<br />
NCO<br />
OCN<br />
Naphthalene 1,5-diisocyanate<br />
Figure 2.4: Aromatic Diisocyanates
Isocyanate<br />
Table 2.1: Isocyanates for Polyurethanes<br />
Hexamethylene diisocyanate<br />
Isophorone diisocyanate<br />
Dicyclohexylmethane-4,4 ′ -diisocyanate<br />
4,4 ′ -Diisocyanato dicyclo hexylmethane<br />
2,4-Toluene diisocyanate<br />
Remarks<br />
Color-free<br />
Color-free<br />
Polyurethanes 73<br />
A mixture of 65% 2,4 isomer <strong>and</strong><br />
35% 2,6 isomer is most common<br />
2,6-Toluene diisocyanate<br />
1,5-Naphthalene diisocyanate<br />
4,4 ′ -Methylene diphenyl diisocyanate Lower volatile then TDI<br />
4,4-Methylene biscyclohexyl diisocyanate<br />
(HMDI)<br />
1,2-Bis(isocyanate)ethoxyethane<br />
(TEGDI)<br />
Extremely soft 18<br />
Macromonomers See Ref. 19<br />
Lysine-diisocyanate Biodegradable formulations 20<br />
detected in a mixture of 2,4 ′ -methylene diphenyl diisocyanate (2,4 ′ -MDI)<br />
<strong>and</strong> 4,4 ′ -methylene diphenyl diisocyanate (4,4 ′ -MDI). Because of the high<br />
reactivity with moisture, the analysis requires special techniques; less than<br />
5 ng/m 3 can be detected. 21<br />
2.2.1.1 Toluene diisocyanate<br />
In technical applications, toluene diisocyanate (TDI) is used either as pure<br />
2,4-isomer or as a blend of the 2,4- <strong>and</strong> 2,6-isomers. Two blend qualities<br />
are available, TDI-80/20 <strong>and</strong> TDI-65/35, which means 80% 2,4-isomer<br />
with 20% 2,6-isomer, <strong>and</strong> 65% 2,4-isomer with 35% 2,6-isomer, respectively.<br />
The two isocyanate groups have unequal reactivity; the isocyanate<br />
group at the p-position is more reactive.<br />
Toluene diisocyanate is synthesized from toluene via dinitrotoluene,<br />
reduction of the nitro group with hydrogen (c.f. Figure 2.5) <strong>and</strong> phosgenation<br />
as shown in Figure 2.1.<br />
The nitration of toluene is achieved in a two-step procedure. In the<br />
first step a mixture of the ortho, para, <strong>and</strong> meta isomers (63% o-isomer,<br />
33% p-isomer, 4% m-isomer) is obtained. The isomers can be separated<br />
by distillation. When p-nitrotoluene is used in the second nitration step, a
74 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
CH 3 CH 3<br />
HNO 3 /H 2 SO 4 O 2 N NO 2<br />
H 2<br />
O<br />
CH 3<br />
NH 2<br />
H 2 N<br />
Cl<br />
C<br />
Cl<br />
OCN<br />
CH 3<br />
NCO<br />
Figure 2.5: First Steps of the Synthesis of Toluene diisocyanate<br />
100% 2,4-dinitrotoluene is obtained. The nitration of o-nitrotoluene finally<br />
yields the TDI-65/35 quality. If the blend obtained from the first step is<br />
directly reacted, the TDI-80/20 quality will be obtained.<br />
2.2.1.2 Diphenylmethane diisocyanate<br />
Diphenylmethane diisocyanate (MDI) has a lower vapor pressure <strong>and</strong> is<br />
therefore less toxic than TDI. The synthesis of MDI starts with the condensation<br />
of aniline with formaldehyde as shown in Figure 2.6 for the ortho<br />
adducts. In fact, 2,2 ′ - <strong>and</strong> 2,4 ′ - <strong>and</strong> 4,4 ′ -isomers are formed, the yield of<br />
the dimer of 4,4 ′ -diphenylmethane diamine being in an amount of ca. 50%.<br />
The isocyanates are obtained then in the usual way by phosgenation. The<br />
crude mixture can be directly used. However, the mixture can be separated<br />
or otherwise modified in order to obtain products with more convenient<br />
properties.<br />
4,4 ′ -MDI has a melting point around 38°C. It forms insoluble dimers<br />
when stored above the melting point. Further, it tends to crystalize. A<br />
mixture of 2,4 ′ -MDI <strong>and</strong> 4,4 ′ -MDI shows a lowering of the melting point<br />
with a minimum of 15°C at 50% p-isomer.<br />
2.2.1.3 Aliphatic Diisocyanates<br />
A disadvantage of aromatic diisocyanates is that they become yellow to<br />
dark brown when they are cured. This limits the fields of applications.
Polyurethanes 75<br />
NH 2<br />
CH 2 NH 2<br />
+<br />
CH 2<br />
O<br />
H 2 N<br />
NH 2 NH 2 NH 2<br />
CH 2 CH 2 CH 2<br />
Figure 2.6: Condensation of Aniline with Formaldehyde<br />
Aliphatic diisocyanates are colorless, but have other disadvantages. In particular,<br />
the mechanical properties of the final products, such as such as<br />
elongation, tensile strength <strong>and</strong> flexibility, are inferior. However, aliphatic<br />
isocyanates find important applications in coating formulations. Aliphatic<br />
diisocyanates include 1,6-hexane diisocyanate (HDI), isophorone diisocyanate<br />
(IPDI), dicyclohexylmethane-4,4 ′ -diisocyanate, i.e., hydrogenated<br />
MDI, c.f. Figure 2.7.<br />
In general, aliphatic are less reactive than aromatic isocyanates. Due<br />
to steric hinderance, the affinity of m-tetramethylxylene diisocyanate to<br />
water is so small that it can be dispersed in water without reacting.<br />
2.2.1.4 Modified Diisocyanates<br />
The isocyanates can be modified in several ways, i.e. by dimerization,<br />
oligomerization with diols, or capping the isocyanate group.<br />
Dimerization. Diisocyanates can be dimerized, by splitting off carbon<br />
dioxide, to the respective carbodiimides. The carbodiimide can react further<br />
with an excess of isocyanate to a uretonimine, c.f. Figure 2.8. Such
76 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
OCN<br />
CH 2 CH 2 CH 2 CH 2 CH 2 CH 2 CH 2<br />
NCO<br />
Hexamethylene diisocyanate<br />
NCO<br />
CH 2<br />
NCO<br />
H 3 C<br />
C CH 3<br />
H 3 C<br />
CH 3<br />
NCO<br />
CH 3<br />
C<br />
NCO<br />
H 3 C<br />
Isophorone diisocyanate<br />
m-Tetramethylxylene diisocyanate<br />
Figure 2.7: Aliphatic Diisocyanates: 1,6-Hexane diisocyanate, Isophorone diisocyanate,<br />
m-Tetramethylxylene diisocyanate<br />
compounds have now three isocyanate groups in the molecule, i.e., they<br />
have a functionality of three.<br />
The properties of MDI can be varied in wide ranges, <strong>and</strong> consequently<br />
can be used for different applications. The crude MDI is used for<br />
rigid foams. Pure 4,4 ′ -MDI is used, among other applications, for shoe<br />
soles <strong>and</strong> also for thermoplastic polyurethanes.<br />
Biuret Reaction. Water hydrolyzes the isocyanate group very quickly.<br />
Therefore it is essential to store the isocyanate material moisture-free. On<br />
the other h<strong>and</strong>, the action of water can be purposefully used to modify<br />
isocyanates. A biuret is formed by the reaction of a substituted urea with<br />
isocyanate, as shown in Figure 2.9. The substituted urea itself can be obtained<br />
by the reaction of water with isocyanate. An amine is formed in the<br />
course of hydrolysis that condenses immediately with water to the substituted<br />
urea. The substituted urea is the reagent for the biuret reaction as<br />
explained above.<br />
Prepolymers. If a glycol or a glycol ether is reacted with an excess<br />
of a diisocyanate, then a prepolymer is formed. In this reaction one diol<br />
couples two molecules of diisocyanate, as schematically shown in Figure<br />
2.10. Also, branched alcohols, like 1,1,1-trimethylolpropane, can be used.
Polyurethanes 77<br />
NCO<br />
NCO<br />
NCO<br />
NCO<br />
CH 2<br />
CH 2<br />
CH 2<br />
CH 2<br />
NCO<br />
N<br />
N<br />
NCO<br />
C<br />
N<br />
C<br />
N<br />
N<br />
C<br />
O<br />
CH 2<br />
CH 2<br />
CH 2<br />
NCO<br />
NCO<br />
NCO<br />
Figure 2.8: Formation of Uretonimine<br />
R N C O<br />
H<br />
N C O<br />
R<br />
N R’<br />
H<br />
R N C O<br />
N C O<br />
R<br />
N R’<br />
Figure 2.9: Biuret Formation of Isocyanates
78 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
OCN<br />
CH 2<br />
NCO<br />
HO<br />
+<br />
CH 2 CH 2 O CH 2 CH 2 OH<br />
H<br />
O<br />
OCN<br />
CH 2<br />
N<br />
C<br />
O<br />
CH 2<br />
CH 2<br />
O<br />
CH 2<br />
CH 2<br />
O<br />
OCN<br />
CH 2<br />
N<br />
C<br />
H<br />
O<br />
Figure 2.10: Formation of Prepolymers
Polyurethanes 79<br />
In this case ideally a trifunctional isocyanate is formed.<br />
When the stoichiometric ratio of isocyanate groups to alcohol groups<br />
is more then two, appreciable amounts of unreacted diisocyanate is left behind,<br />
which causes an increased toxicity. If the diisocyanate is sufficiently<br />
volatile, the unreacted residual diisocyanate can be removed by distillation<br />
under vacuum. Such mixtures are liquids at room temperature. Because of<br />
larger structure the prepolymers are less volatile <strong>and</strong> therefore less toxic.<br />
Toluene diisocyanate <strong>and</strong> isophorone diisocyanate possess two isocyanate<br />
groups with different reactivities. When forming the prepolymer,<br />
the more reactive group is reacted. The less reactive group is left unreacted.<br />
The properties of the final product can be adjusted by the selection<br />
of the components <strong>and</strong> the amounts making the prepolymer. For example,<br />
prepolymers based on poly(ethylene oxide) or poly(propylene oxide) will<br />
be used for hydrophilic gels, whereas hydrophobic polyols will result in<br />
hydrophobic polyurethanes. For hydrophobic polyurethanes, polyols with<br />
very nonpolar backbones, e.g., hydroxyl functional poly(butadiene), can<br />
be used to introduce the hydrophobicity. 22<br />
By choosing the stoichiometric ratio of NCO to OH groups, the content<br />
of free isocyanate groups can be adjusted from 2% to 20%.<br />
Viscosity is an important parameter for the processability of the raw<br />
materials. The viscosity increases with molecular weight <strong>and</strong> decreases<br />
with the content of unreacted isocyanate. The viscosity also increases with<br />
increasing allophanate formed, because this is a crosslinking reaction. The<br />
allophanate formation is favored at temperatures above 60 to 80°C <strong>and</strong> catalyzed<br />
by alkaline residues in polyether polyols, if any is present. Therefore,<br />
to increase the storage time of the prepolymer, acid stabilizers such as<br />
benzoyl chloride, acetyl chloride, or p-toluenesulfonic acid can be added.<br />
End-capped Diisocyanates. The reaction of the isocyanate group with<br />
alcohols to form the urethane functionality is thermoreversible. At elevated<br />
temperatures the urethane decomposes into the isocyanate. This reaction<br />
is utilized at the phosgene-free route of synthesis of isocyanates. On the<br />
other h<strong>and</strong>, the reversibility can be used in the preparation of end-capped,<br />
or blocked diisocyanates.<br />
The isocyanate group is allowed to react with compounds containing<br />
acidic hydrogen atoms. In this way the isocyanate group is masked <strong>and</strong> not<br />
accessible for other reactants. At elevated temperatures the retro reaction<br />
takes place, the isocyanate group is set free, <strong>and</strong> in presence of amines the
80 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
urethane can be formed. A necessary condition for the concept to work<br />
properly is that the unblocking reaction takes places at lower temperatures<br />
than the thermal decomposition of the urethane group.<br />
The temperatures for the retro reaction of unblocking are between 90<br />
<strong>and</strong> 160°C. Aromatic isocyanates are less stable than aliphatic isocyanates.<br />
The temperature of unblocking decreases in the following order for the<br />
types of blocking agents: alcohols > lactams > ketoximes > active methylene<br />
groups containing compounds. Suitable blocking agents are phenol,<br />
ethyl acetoacetate, ε-caprolactam, methylethylketoxime, diethyl malonate,<br />
<strong>and</strong> 3,5-dimethylpyrazole.<br />
N,N ′ -Carbonylbiscaprolactam (CBC), c.f. Figure 2.11, offers an isocyanate-free<br />
route to new families of thermosets <strong>and</strong> reactive resins with<br />
caprolactam-blocked isocyanates. CBC reacts with primary amines into<br />
blocked isocyanates at 100 to 150°C. The reaction is also suitable for<br />
highly functional amine dendrimers <strong>and</strong> polymers.<br />
With polyols, a ring-opening of the caprolactam occurs. Catalysts<br />
include zirconium alcoholates, magnesium bromide or dibutyltin dilaurate<br />
(DBTDL). N-carbamoyl caprolactam end groups are formed by a nucleophilic<br />
attack of the hydroxy group at one of the CBC caprolactam rings <strong>and</strong><br />
subsequent ring opening. Thus, the corresponding blocked ester-functional<br />
isocyanates are formed.<br />
The CBC derivatives are attractive crosslinking agents <strong>and</strong> interfacial<br />
coupling agents for adhesives <strong>and</strong> coatings. Further, due to the<br />
non-toxic CBC-intermediates <strong>and</strong> polyesterurethanes, they are also suitable<br />
for medical applications. 23, 24 When the ring opening reaction is done<br />
with poly(propylene oxide)-based triols, then crosslinked polyurethanes<br />
are obtained. 25 Thus, 1,2-bis-[2(2-hydroxy-5-methylphenyl)-5-benzotriazolyl]-ethane<br />
(BHMBE) reacts with the phenolic hydroxyl groups <strong>and</strong> is<br />
thus a reactive UV-absorber. 26 The synthesis starts from 4,4 ′ -diaminodibenzyl<br />
in several steps. The structure is shown in Figure 2.12.<br />
Isocyanurate. The formation of an isocyanurate is in fact a trimerization<br />
of an isocyanate (Figure 2.13). Trimers from toluene diisocyanate <strong>and</strong><br />
hexamethylene diisocyanate are available. Such isocyanate isocyanurate<br />
structures are trifunctional, i.e., they have three isocyanate groups pending.<br />
They can be modified to become more hydrophilic, if one isocyanate<br />
group is allowed to be coupled with a polyglycol, e.g., poly(ethylene oxide)<br />
or poly(propylene oxide).
Polyurethanes 81<br />
O<br />
R X C N +<br />
O<br />
O<br />
N<br />
H<br />
O<br />
N<br />
C<br />
N<br />
+ RXH<br />
O<br />
O<br />
R<br />
X<br />
H<br />
N<br />
C<br />
N<br />
O<br />
O<br />
O<br />
Figure 2.11: Reaction of N,N ′ -Carbonylbiscaprolactam with a Nucleophile RXH.<br />
Top: ring elimination with formation of caprolactam. Bottom: ring opening reaction.<br />
23 CH 2 CH 2<br />
OH<br />
N<br />
N<br />
N<br />
N<br />
N<br />
N<br />
HO<br />
H 3 C CH 3<br />
Figure 2.12: 1,2-Bis-[2(2-hydroxy-5-methylphenyl)-5-benzotriazolyl]-ethane 26
82 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
3 R NCO<br />
R<br />
N<br />
N<br />
R<br />
O<br />
N<br />
O<br />
R<br />
Figure 2.13: Trimerization: Formation of an Isocyanurate Structure<br />
Macromonomers. A macromonomer is a polymer that contains reactive<br />
groups, here isocyanate groups. A macromonomer from 2-(dimethylamino)ethyl<br />
methacrylate that bears a 1-(isopropenylphenyl)-1,1-dimethylmethyl<br />
isocyanate group has been synthesized. However, 2-(dimethylamino)ethyl<br />
methacrylate (DMAEMA) reacts with 2-mercaptoethanol<br />
preferably in an addition reaction that acts as chain transfer agent in radical<br />
telomerization. In this way, an adduct of the methacrylate <strong>and</strong> the mercapto<br />
compound is formed. The structure of the adduct <strong>and</strong> the product<br />
of functionalization are shown in Figure 2.14. The oligomers can be then<br />
functionalized with 1-(isopropenylphenyl)-1,1-dimethylmethyl isocyanate<br />
(TMI), resulting in macromonomers. 19<br />
α,α ′ -Dihydroxyl-poly(butyl acrylate) prepared by atom transfer radical<br />
polymerization (ATRP) has been used as a macromonomer with two<br />
hydroxyl groups at one end. This macromonomer was used for chain extension<br />
of diphenyl-methane-4,4-diisocyanate to obtain comb-like oligo<br />
isocyanates, as shown in Figure 2.15. These materials have potential interest<br />
as pressure-sensitive adhesives (PSA). 27<br />
In a completely different way rodlike macromonomers were obtained.<br />
In a first step, the N=C bond n-hexyl isocyanate was polymerized<br />
by titanium catalysts in a living polymerization. The living chain end was<br />
deactivated by methacryloyl chloride to result in a methacrylic-terminated<br />
poly(n-hexyl isocyanate. 28<br />
Block copolymers from n-hexyl isocyanate <strong>and</strong> isoprene have been<br />
obtained by a living polymerization technique. 29 The living anionic polymerization<br />
proceeds very fast <strong>and</strong> therefore low temperatures −98°C, are<br />
required to control the selectivity. 3,5-Bis(4-aminophenoxy)benzoic acid,<br />
c.f. Figure 2.16, is a monomer from the type AB 2 . It can be polycondensed<br />
to form dendritic polymers. These polymers contain pendant amino groups<br />
that can be crosslinked with diisocyanates. 30
Polyurethanes 83<br />
O<br />
O<br />
S<br />
CH 2<br />
H<br />
CH 2<br />
CH C<br />
CH 3<br />
O<br />
CH 2<br />
CH 2 CH 2<br />
S<br />
CH 3<br />
C<br />
O<br />
CH 2<br />
CH 2<br />
CH 2<br />
CH 2<br />
CH 2<br />
OH<br />
N<br />
H 3 C CH 3<br />
CH 2<br />
OH<br />
N<br />
H 3 C CH 3<br />
H 2 CH<br />
CH 3<br />
C<br />
CH 3<br />
O<br />
S<br />
CH 2<br />
CH 2 CH 2<br />
CH 3<br />
O<br />
C<br />
O<br />
CH 2<br />
C<br />
NH<br />
C<br />
O<br />
CH 2<br />
CH 2<br />
CH 3<br />
N<br />
H 3 C CH 3<br />
Figure 2.14: Adduct from 2-(dimethylamino)ethyl methacrylate <strong>and</strong> 1-(isopropenylphenyl)-1,1-dimethylmethyl<br />
isocyanate 19<br />
CH 3<br />
N<br />
H<br />
O<br />
C<br />
CH 2 O<br />
O CH 2 C CH 2 O C N CH 2 NCO<br />
CH 2 H<br />
O<br />
O CH 2 CH 2 CH 2 CH 3<br />
O C<br />
C O<br />
H 3 C C CH 2 CH CH 2 CH<br />
CH 3 C O<br />
O CH 2 CH 2 CH 2 CH 3<br />
Figure 2.15: Comb-like Oligo Isocyanates 27
84 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
H 2 N<br />
H 2 N<br />
O<br />
O<br />
O<br />
C<br />
OH<br />
Figure 2.16: 3,5-Bis(4-aminophenoxy)benzoic acid<br />
2.2.1.5 Enzymatic Synthesis of Polyurethanes<br />
Polyurethanes have been synthesized using the enzyme C<strong>and</strong>ida antarctica<br />
lipase B. The use of enzymatic methods offers the possibility to reverse the<br />
conventional process by creating the urethane first <strong>and</strong> then using a low<br />
temperature enzymatic polyester synthesis to build the polymer. A novel<br />
series of biscarbamate esters <strong>and</strong> polyesters also could be obtained. 31<br />
2.2.1.6 Synthesis of Urethanes via Carbonate Esters<br />
The synthesis of urethanes avoiding h<strong>and</strong>ling of isocyanates is also possible<br />
by the reaction of amines or diamines with ethylene carbonate. The<br />
scheme is shown in Figure 2.17. Urethane dimethacrylates suitable for<br />
dental fillers have been synthesized in this way. For example, ethylene<br />
carbonate in two-fold excess was reacted with 1,6-hexane diamine to obtain<br />
a urdiol. This was reacted with methacrylic anhydride. 32<br />
2.2.2 Polyols<br />
Polyols are the second basic component beside diisocyanates. There are<br />
two types of polyols,<br />
1. Polyether polyols,<br />
2. Polyester polyols.<br />
2.2.2.1 Polyether Polyols<br />
Most widely used are polyether polyols. Monomers commonly used for<br />
polyether polyols are listed in Table 2.2.
Polyurethanes 85<br />
O<br />
O<br />
O<br />
HO(CH 2 ) 2 O<br />
H 2 N<br />
NH 2<br />
O<br />
CH 2<br />
H 2 C<br />
O<br />
CH 2<br />
H 2 C<br />
O<br />
O<br />
C HN NH C O(CH 2 ) 2 OH<br />
O<br />
Figure 2.17: Reaction of Ethylene Carbonate with 1,6-Hexane diamine<br />
Table 2.2: Monomers for Polyether Polyols<br />
Monomer<br />
Propylene oxide<br />
Ethylene oxide<br />
Butylene oxide<br />
Tetrahydrofuran<br />
Remarks<br />
As copolymer with propylene oxide<br />
In fibers <strong>and</strong> elastomers
86 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
R OH + B R O<br />
O<br />
R O + CH 2 CH 2<br />
CH 3<br />
R<br />
O<br />
CH 2<br />
CH 2 O<br />
CH 3<br />
Figure 2.18: Initial Steps of the Formation of Polyether polyols<br />
Anionic Ring Opening. Polyols with a molecular weight between 1,000<br />
<strong>and</strong> 6,000 Dalton <strong>and</strong> a functionality between 1.8 <strong>and</strong> 3.0 are used in flexible<br />
foams <strong>and</strong> elastomers. Polyols with a molecular weight below 1,000<br />
Dalton <strong>and</strong> high functionalities result in high crosslinked rigid chains <strong>and</strong><br />
are used in rigid foams <strong>and</strong> high performance coatings.<br />
The polymerization is initiated with an alcohol <strong>and</strong> a strong base.<br />
The base is usually potassium hydroxide that forms initially the monomeric<br />
alcoholate. The alcoholate anion is subjected to a series of ring opening reactions<br />
of the epoxide or the cyclic ether. The basic mechanism is sketched<br />
in Figure 2.18.<br />
In the case of nonsymmetric epoxides the alcoholate anion attacks<br />
the less hindered carbon atom of the epoxide, as shown in Figure 2.18.<br />
Therefore, polyols composed exclusively from propylene oxide bear<br />
secondary hydroxyl groups as end groups. Secondary hydroxyl groups are<br />
less reactive than primary hydroxyl groups.<br />
To get polyols with the more reactive primary hydroxyl groups, the<br />
polymerization is started with propylene oxide, <strong>and</strong> in the final stage ethylene<br />
oxide is added. Ethylene oxide improves the water solubility of the<br />
polyol.<br />
Due to the mechanism of polymerization without termination in preparing<br />
polyether polyols, the molecular weight distribution of the polyols<br />
exhibits a Poisson distribution. This is narrower than the distribution of<br />
polyester polyols. Instead of alcohols, amines can also be used. Typical<br />
initiator alcohols are propylene glycol, glycerol, trimethylolpropane, triethanolamine,<br />
pentaerythritol, sorbitol, or sucrose.<br />
Sucrose results in highly branched polyols suitable for rigid foams,<br />
whereas the alcohols with a lower functionality are used for flexible materials.<br />
Amines include ethylene diamine, toluene diamine, 4 ′ ,4 ′ -diphenyl-
Polyurethanes 87<br />
methane diamine, <strong>and</strong> diethylenetriamine. The resulting polyols exhibit a<br />
higher basicity than the polyols with an alcohol as initiator <strong>and</strong> are therefore<br />
more reactive with isocyanates.<br />
A side reaction of the base in polymerization is the isomerization<br />
reaction. For example, propylene oxide isomerizes to allyl alcohol. As a<br />
consequence, vinyl-terminated monofunctional polyols are formed. Such<br />
monofunctional polyols are addressed as monols. Such compounds have<br />
negative influence on the mechanical properties of the final products.<br />
The formation of monols can be suppressed by using special catalysts,<br />
e.g., zinc hexacyanocobaltate. This type of catalyst is referred to as<br />
double metal cyanide catalyst.<br />
Grafted Polyols. Copolymer polyols are obtained by grafting styrene<br />
or acrylonitrile to poly(propylene oxide). The radicals attack the tertiary<br />
hydrogen sites (−CH 2 CH tert (−CH 3 )−O) in the poly(propylene oxide) as<br />
a transfer reaction to the poly(propylene oxide). Originally pure acrylonitrile<br />
was used for grafting, but the so formed copolymer polyols cause<br />
discoloration problems in slabstock flexible foams. For this reason styrene/acrylonitrile<br />
copolymer polyols were developed.<br />
Vinyl Functionalized Polyols. Another method is to functionalize the<br />
polyols with a vinyl moiety. This is achieved by reaction of the polyols<br />
with maleic anhydride, or methacryloyl chloride. Of course the functionality<br />
of the polyols must be greater than two with respect to the hydroxyl<br />
group, because hydroxyl groups are lost. If to the vinyl functionalized<br />
polyol a polymerizing vinyl monomer mixture is added, the pendent vinyl<br />
group polyols take part in the polymerization reaction. With respect to the<br />
vinyl polymer a comb-like structure is formed, the teeth of the “comb” being<br />
the polyol moieties. The styrene is hydrophobic, <strong>and</strong> at higher conversion<br />
the backbone of the comb may collapse to yield a spherical structure.<br />
The polyol chains are at the surface of the sphere.<br />
Polyurea-modified Polyols. Urea urethane polyols <strong>and</strong> polyurea-modified<br />
polyols are another type of polyols. They are synthesized in a twostage<br />
reaction.<br />
1. In the first stage a diamine or an amino alcohol is allowed to react<br />
with an excess of diisocyanate. The amine groups react with
88 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
the isocyanate group to form urea groups, whereas the hydroxy<br />
groups react with the isocyanate group to form urethane groups.<br />
The excess of isocyanate causes the formation of an isocyanate<br />
end-capped prepolymer. In the case of a diamine, isocyanates are<br />
formed that contain exclusively urea groups in their backbone. In<br />
the case of amino alcohols isocyanates containing urea <strong>and</strong> urethane<br />
in the backbone are formed. Suitable diamines are hydrazine,<br />
ethylene diamine, etc.<br />
2. In the second stage a diol or a polyol in molar excess with respect<br />
to the unreacted isocyanate groups is added. The pending isocyanate<br />
groups react with the hydroxy groups to form chain-extended<br />
polymeric polyols. The reaction of diamines with isocyanates proceeds<br />
fast in comparison to the reaction of polyols with isocyanates.<br />
Autocatalytic Polyols. The alkylamine group can be introduced in a<br />
polyol chain by using N-alkylaziridine or N,N-dialkyl glycidylamine as<br />
a comonomer with ethylene oxide or propylene oxide. Since the amine<br />
groups in the chain catalyze the reaction of the hydroxyl groups with the<br />
isocyanate, this type of polyol is called autocatalytic. 33<br />
Autocatalytic polyols require less capping with primary hydroxyls,<br />
that is, less ethylene oxide capping to obtain the same performance in flexible<br />
molded foam than conventional polyols when used under the same<br />
conditions. Moreover, low emission polyurethane polymers can be made<br />
with autocatalytic polyols.<br />
2.2.2.2 Polyester Polyols<br />
Typical monomer combinations for polyester polyols are shown in Table<br />
2.3.<br />
Polyesters from Acid <strong>and</strong> Alcohols. The polyesters are produced by preheating<br />
the diol to ca. 90°C <strong>and</strong> adding the acid into it. The reaction temperature<br />
is raised gently up to 200°C to completion. Inert gas or vacuum<br />
is used to remove the water. The condensation is an equilibrium reaction,<br />
<strong>and</strong> a Schulz-Flory distribution of the molecular weight is obtained.<br />
The condensation is catalyzed by acids, bases, <strong>and</strong> transition metal<br />
compounds. However, catalysts should be used with care, because they
Polyurethanes 89<br />
Table 2.3: Monomers for Polyester Polyols<br />
Acid Alcohol Components<br />
Uses<br />
Adipic acid, diethylene glycol, 1,1,1-trimethylolpropane<br />
Flexible foam<br />
Adipic acid, phthalic acid, 1,2-propylene glycol, glycerol<br />
Semi-rigid foam<br />
Adipic acid, phthalic acid, oleic acid, 1,1,1-trimethylolpropane<br />
Rigid foam<br />
Adipic acid, ethylene glycol, diethylene glycol Shoe soles<br />
Adipic acid, ethylene glycol, 1,4-butanediol Elastomers<br />
ε-caprolactone, various diols<br />
Ring opening condsation<br />
Castor oil, glycerol, trimethylolpropane<br />
Transesterification<br />
could have undesirable effects on the subsequent curing reaction. Condensation<br />
catalysts based on tin <strong>and</strong> other transition metals added only in<br />
the ppm range did not show negative effects on the later procedures <strong>and</strong><br />
properties.<br />
The hydroxyl numbers increase from flexible foams to rigid foams<br />
from 60 mgKOH/g up to 400 mgKOH/g. Acids for soft foams are aliphatic<br />
acids, such as adipic acid, whereas phthalic anhydride increases the<br />
rigidity.<br />
Terephthalic acid or isophthalic acid are used in high performance<br />
hard coatings <strong>and</strong> adhesives. Such foams are improved to be flame resistant.<br />
Foams based on aromatic polyester polyols show charring upon<br />
exposure to flame.<br />
Polyesters based on terephthalic acid are manufactured by transesterification<br />
of dimethyl terephthalate. Also poly(ethylene terephthalate)<br />
waste materials, such as polyester fibers or soft drink bottles, can be recycled<br />
by glycolysis to obtain suitable polyols.<br />
Triols, such as glycerol <strong>and</strong> 1,1,1-trimethylolpropane, will result<br />
in branched polyesters. Alcohols for flexible foams are ethylene glycol,<br />
diethylene glycol, propylene glycol, 1,4-butanediol, 1,6-hexanediol, etc.<br />
Longer chains result in a greater hydrolytic stability, simply because there<br />
are fewer ester groups in the structure.<br />
Polyesters from a single acid component <strong>and</strong> a single alcohol component<br />
are crystalline. The crystallinity can be reduced by using mixtures<br />
of diols or mixtures of different polyesters.
90 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Mixed polyesters from waste acids of the production of nylon contain<br />
adipic acid, glutaric acid, <strong>and</strong> succinic acid. The acids can be also<br />
hydrogenated to obtain the respective diols that can be used in the condensation.<br />
The ester group in polyester polyols is sensitive to hydrolysis attack.<br />
The hydrolysis stability can be improved with additives that react<br />
with carboxylic <strong>and</strong> alcoholic groups, which are formed during the hydrolysis.<br />
These additives include oxazolines, epoxy compounds, <strong>and</strong> carbodiimide<br />
structures. In particular, polyester polyols can be stabilized by the<br />
addition of 1 to 2% of hindered aromatic carbodiimides. These compounds<br />
are scavengers for the acid generated by ester hydrolysis. The acid would<br />
catalyze further hydrolysis.<br />
Polyester polyols can contain 10 to 20% of vinyl polymers. The<br />
vinyl polymers improve the hydrolysis stability, hardness <strong>and</strong> the form stability.<br />
ε-Caprolactone based polyesters. Another synthesis route for aliphatic<br />
polyester polyols is the ring opening polymerization of ε-caprolactone with<br />
various glycols.<br />
These include diethylene glycol, 1,4 butanediol, neopentyl glycol, or<br />
1,6-hexanediol. Branched products are obtained by adding 1,1,1-trimethylolpropane<br />
or glycerol to a bifunctional alcohol. Higher branched polyesters<br />
utilize pentaerythritol. The poly(ε-caprolactone)-containing polyesters<br />
exhibit a greater hydrolysis resistance <strong>and</strong> lower viscosity than comparable<br />
polyadipate glycols.<br />
2.2.3 Other Polyols<br />
2.2.3.1 Hydrocarbon Polyols<br />
Hydrocarbon polyols can be obtained by living anionic polymerization of<br />
butadiene initiated by sodium naphthalene, which is the common route to<br />
polymerize butadiene. However, the living chains are finally terminated by<br />
adding ethylene oxide or propylene oxide. By adding water a poly(butadiene)<br />
with primary <strong>and</strong> secondary hydroxyl groups is obtained.<br />
Hydroxy-terminated poly(butadiene) is also accessible by free-radical<br />
polymerization of butadiene, initiated by hydrogen peroxide. The major<br />
advantage of hydrocarbon polyols is the high chemical resistance. The<br />
low glass transition temperature keeps its elastomeric properties down to
Polyurethanes 91<br />
extremely low temperatures. The double bonds in the chain or pendent<br />
double bonds open the possibility of further reactions, like vulcanization<br />
<strong>and</strong> other chemical reactions. The functionality of these diols is two, therefore<br />
they can be used for thermoplastic polyurethanes.<br />
2.2.3.2 Polythioether Polyols<br />
Polythioether polyols include products obtained by condensing thiodiglycol<br />
either alone or with other glycols, alkylene oxides, dicarboxylic acids,<br />
formaldehyde, amino-alcohols, or aminocarboxylic acids.<br />
2.2.3.3 Polyacetal Polyols<br />
Polyacetal polyols are prepared by reacting glycols such as diethylene glycol,<br />
triethylene glycol, or hexanediol with formaldehyde. Suitable polyacetals<br />
may also be prepared by polymerizing cyclic acetals.<br />
2.2.3.4 Acrylic Polyols<br />
Acrylic polyols are obtained by copolymerization of acrylic monomers,<br />
such as ethyl acrylate, n-butyl acrylate, acrylic acid, methyl methacrylate,<br />
or styrene with minor amounts of 2-hydroxyethyl acrylate or 4-hydroxybutyl<br />
acrylate. Styrene, if added, makes the acrylic polyol more hydrophobic.<br />
Acrylic polyols are used in two-component coating systems. They<br />
exhibit good chemical resistance <strong>and</strong> weatherability.<br />
2.2.3.5 Liquefied Wood<br />
Liquefied wood can be obtained by the liquefaction of benzylated wood<br />
wastes using dibasic esters as solvent with hydrochloric acid as catalyst.<br />
The reaction is completed at 80°C after 3 hours. Liquefied wood acts as<br />
a diol component for, e.g., TDI, IPDI, <strong>and</strong> HDI. Polyurethane resins from<br />
liquefied wood have a higher thermal stability than the traditional polyurethane<br />
resins. 34<br />
2.2.4 Polyamines<br />
The amine functionality reacts with the isocyanate group to a urea moiety.<br />
In this way an amine group corresponds to a hydroxy group that reacts with<br />
the isocyanate group to a urethane moiety.
92 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Hydroxyl end groups in polyether polyols can be converted into amine<br />
end groups by reductive amination. This type of compound is called an<br />
amine-terminated polyether, or simply polyetheramine. Polyetheramines<br />
are suitable for soft segments of polyurea resins.<br />
2.2.5 Chain Extenders<br />
Chain extenders, curing agents, <strong>and</strong> crosslinkers are low molecular compounds<br />
for improving properties of the final products. Examples are shown<br />
in Table 2.4. Chain extenders are difunctional compounds. Glycols are<br />
used in polyurethanes. Diamines or hydroxylamines are used in polyureas<br />
<strong>and</strong> mixed polyurethane ureas. Low-molecular weight polyamines react<br />
with the isocyanate group very fast, <strong>and</strong> can be used in reactive injection<br />
molding, where short cycles are essential.<br />
2,2 ′ -Pyromellitdiimidodisuccinic anhydride (DA) can act as a chain<br />
extender for isocyanates in the presence of polyols. In a first stage, the<br />
polyol is allowed to react with the isocyanate compound to get isocyanateterminated<br />
oligomers. In the second stage, the 2,2 ′ -pyromellitdiimidodisuccinic<br />
anhydride reacts with the oligomer, splitting off carbon dioxide to<br />
result in a poly(urethane-imide-imide). This class of polyurethane has a<br />
higher thermal stability than conventional polyurethanes. 35<br />
Chain extenders with the triazene structure are photosensitive compounds.<br />
36 They are used together with another extender as a coextender.<br />
Because the resulting triazene polyurethanes become crosslinked by exposure<br />
to UV irradiation, they have a potential use as negative-resist polymers.<br />
2.2.6 Catalysts<br />
Catalysts are necessary to obtain the desired end products. The final properties<br />
depend strongly on the content of urethane, urea, allophanate, biuret,<br />
<strong>and</strong> isocyanurate bonds. Therefore, catalysts govern the final properties of<br />
the materials. The nature of the catalysts also greatly influences the reaction<br />
time <strong>and</strong> the properties of the final product. The catalysts can be<br />
classified into three main categories:<br />
1. Catalysts for blowing,<br />
2. Catalysts for gelling, <strong>and</strong><br />
3. Catalysts for crosslinking.
Polyurethanes 93<br />
Compound<br />
Ethylene glycol<br />
Diethylene glycol<br />
Propylene glycol<br />
Dipropylene glycol<br />
1,4 Butanediol<br />
2-Methyl-1,3-propylene diol<br />
N,N ′ -bis(2-hydroxypropylaniline)<br />
Water<br />
1,4-Di(2-hydroxyethyl)hydroquinone<br />
Diethanolamine<br />
Triethanolamine<br />
1,1,1-Trimethylolpropane<br />
Glycerol<br />
Dimethylol butanoic acid (DMBA)<br />
Table 2.4: Chain Extenders<br />
Hydrazine<br />
Ethylene diamine (EDA)<br />
1,4-Cyclohexane diamine<br />
Isophorone diamine<br />
4,4 ′ -bis(sec-Butylamine)dicyclohexylmethane<br />
4,4 ′ -bis(sec-Butylamine)diphenylmethane<br />
Diethyltoluene diamine<br />
4,4 ′ -Methylene bis(2-chloroaniline)<br />
4-Chloro-3,5-diamino-benzoic acid isobutylester<br />
3,5-Dimethylthio-toluene diamine<br />
Trimethylene glycol-di-p-aminobenzoate<br />
4,4 ′ -Methylene bis(3-chloro-2,6-diethylaniline)<br />
1-(α-Naphthyl)-3,3-di(2-hydroxyethyl)-<br />
triazene-1 (NT-D)<br />
1-Phenyl-3,3-di(2-hydroxyethyl)-<br />
triazene-1 (PT-D)<br />
Remarks<br />
Waterborne chain extender<br />
37<br />
Both isomers<br />
Both isomers<br />
Photosensitive 36<br />
Photosensitive 36
94 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 2.5: Catalysts Classified According to the Reaction<br />
Reaction<br />
Catalyst Type<br />
Trimerization Strong bases, quaternary ammonium salts, phosphines<br />
Dimerization Phosphorous compounds<br />
Polymerization Alkaline metal hydroxides<br />
Addition to alcohols Tertiary amines, organometals, metal salts<br />
Reaction with water Tertiary amines<br />
Addition to urethane Metal salts<br />
Addition to amines Tin <strong>and</strong> zinc salts<br />
From the chemical view, catalysts for producing polyurethanes can be divided<br />
into two general types: tertiary amines <strong>and</strong> organo-tin compounds.<br />
Organometallic tin catalysts predominantly favor the gelling reaction,<br />
while amine catalysts exhibit a more varied range of blow/gel balance.<br />
A lot of catalysts have been described <strong>and</strong> reviewed. 6, 38 The choice<br />
of the catalyst depends on which reaction <strong>and</strong> which structure is to be favored.<br />
Table 2.5 lists types of catalysts that are suitable for the individual<br />
reactions.<br />
It is important to tune the kinetics of the individual reactions properly.<br />
For example, if the blowing reactions take place significantly before<br />
the sufficient progress of gelling (crosslinking), the viscosity of the reacting<br />
material is low, causing the carbon dioxide to escape, <strong>and</strong> will not yield<br />
a foam.<br />
On the other h<strong>and</strong>, if the gelling (or crosslinking reaction) occurs too<br />
fast, the blowing gas cannot exp<strong>and</strong> the material. Thus, it is necessary to<br />
balance the individual reactions. This balance can be readily controlled by<br />
the nature <strong>and</strong> quantity of the catalyst used.<br />
2.2.7 Blowing<br />
Chemical blowing is effected by the reaction of isocyanate <strong>and</strong> water. The<br />
rate of blowing increases with the catalyst <strong>and</strong> water content. 39 As an<br />
intermediate, carbamic acid is formed. The carbamic acid is not stable; it<br />
decomposes into an amine <strong>and</strong> carbon dioxide. Carbon dioxide exp<strong>and</strong>s<br />
the polyurethane into a foam.<br />
There are also physical blowing agents available. In this case the<br />
foam is generated by the evaporation of the blowing agent supported by
Polyurethanes 95<br />
external heating but also by the temperature rise due to the formation of the<br />
polyurethane from the diisocyanate <strong>and</strong> the polyol. Suitable reagents for<br />
physical blowing were previously fluorocarbons <strong>and</strong> chlorofluorocarbons.<br />
The latter class of substance has been removed because of its ozone depletion<br />
potential. Pentane is a substitute for chlorofluorocarbons. The release<br />
of the physical blowing agents occurs in three ways when a foamed material<br />
is recycled or shredded: 40<br />
1. The instantaneous release from cells split or damaged by the shredding,<br />
2. The short-term release from cells adjacent to the cut surface , <strong>and</strong><br />
3. The long-term release by normal diffusion processes.<br />
Formic acid has been proposed as a chemical blowing agent.<br />
41, 42<br />
Formic acid can behave either as an acid or an aldehyde. In contrast to<br />
water that yields exclusively carbon dioxide, formic acid upon contact with<br />
an isocyanate group reacts to initially liberate carbon monoxide <strong>and</strong> further<br />
decomposes to form an amine with a release of carbon dioxide, according<br />
to the following reaction:<br />
2Φ−NCO+HCOOH → CO+CO 2 + Φ−NH−CO−NH−Φ (2.1)<br />
Aside from its zero ozone depletion potential, a further advantage of using<br />
formic acid is that 2 mol of gas are released for every mole of formic acid<br />
present, whereas a water-isocyanate reaction results in the release of only<br />
1 mol of gas per mol of water. In both the water-isocyanate <strong>and</strong> the formic<br />
acid-isocyanate reactions, the isocyanate is consumed <strong>and</strong> one must add a<br />
proportionate excess of isocyanate to compensate for the loss. However,<br />
since formic acid is a more efficient blowing agent than water, the number<br />
of moles of formic acid necessary to produce the same number of moles of<br />
gas as a water-isocyanate reaction is greatly reduced, thereby reducing the<br />
amount of excess isocyanate <strong>and</strong> leading to a substantial economic advantage.<br />
43 It is believed that liberation of carbon monoxide <strong>and</strong> subsequently<br />
carbon dioxide in the reaction Eq. 2.1 proceeds at a slower rate than the<br />
release of carbon dioxide in a water-isocyanate reaction for two reasons:<br />
1. The anhydride is more stable than the carbamic acid formed in<br />
a water-isocyanate reaction <strong>and</strong>, therefore, requires more thermal<br />
energy to decompose, <strong>and</strong>
96 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
2. The reaction is a two-step reaction rather than the one-step reaction<br />
present in a water-isocyanate reaction.<br />
The exothermic reaction in a polyol composition containing formic acid<br />
proceeds in a more controlled manner than in an all water blown reaction.<br />
Formic acid in combination with hydrochlorofluorocarbons improves<br />
the mechanical <strong>and</strong> thermal properties. It exhibits a delayed action <strong>and</strong><br />
thus a prolonged gel time. Rigid foams produced with formic acid possess<br />
excellent dimensional stability at low densities. 43 However, the generation<br />
of carbon monoxide during the curing <strong>and</strong> corrosion problems are evident<br />
drawbacks.<br />
2.2.7.1 Gelling <strong>and</strong> Crosslinking<br />
Gelling reactions are discussed as curing reactions that do not blow, but<br />
yield linear urethanes. These reactions are similar to crosslinking reactions,<br />
from the chemical view. The technical term “curing” is not common<br />
in polyurethanes, except for unsaturated polyester technology, epoxies,<br />
etc., because the resulting final products are often not hard, e.g., flexible<br />
foams.<br />
The basic reactions in the course of polyurethane formation are shown<br />
in Figure 2.19. These include the reaction of isocyanate with a polyol<br />
to yield a polyurethane, the formation of urea from an isocyanate <strong>and</strong> an<br />
amine, <strong>and</strong> the blowing reaction. Other reactions are the formation of a<br />
biuret, c.f. Figure 2.9 <strong>and</strong> the trimerization, c.f. Figure 2.13.<br />
The action of a catalyst can be studied conveniently with model compounds.<br />
Suitable experimental techniques are liquid chromatography,infrared<br />
spectroscopy, <strong>and</strong> nuclear magnetic resonance spectroscopy. Infrared<br />
spectroscopy conveniently monitors the disappearance of the isocyanate<br />
group.<br />
Raman spectroscopy is advantageous in two ways. Since the Raman<br />
effect is a scattering process, samples of any shape or size can be examined.<br />
Moreover, Raman spectroscopy measurements can be conducted remotely<br />
using inexpensive, communications grade, fused-silica optical fibers. 44<br />
Nuclear magnetic resonance spectroscopy suffers from the disadvantage<br />
that the spectroscopic shifts of the urethane, urea, allophanate, <strong>and</strong><br />
biuret linkages are very similar.<br />
Rheological techniques are also suitable for monitoring the progress<br />
of curing. 45–47 The dynamic viscosity has been measured as a function of
Polyurethanes 97<br />
R N C O<br />
H O R’<br />
R N C O<br />
H O R’<br />
R N C O<br />
H N R’<br />
R N C O<br />
H N R’<br />
R N C O<br />
H O H<br />
R N C O<br />
H O H<br />
R<br />
H<br />
N<br />
H<br />
CO 2<br />
R N C O<br />
H<br />
N C O<br />
R<br />
O R’<br />
H<br />
R N C O<br />
N C O<br />
R<br />
O R’<br />
Figure 2.19: Basic Reactions in Polyurethane Formation: Reaction of Isocyanate<br />
with a Polyol; Formation of Urea from Isocyanate <strong>and</strong> Amine; Chemical Blowing<br />
with Water; Allophanate formation
98 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
time <strong>and</strong> found to be independent of the shear rate. 47 A simple technique of<br />
this kind is to drop metal ball bearings consecutively into a growing foam.<br />
The position of the ball bearings in the final foam reflects the viscosity<br />
profile. The simultaneous measurement of the height of the foam gives<br />
information of the degree of expansion.<br />
The gel times can be used to evaluate the activity of catalysts. In particular,<br />
it was found that the activity of catalysts, among them organometallic<br />
catalysts, decreases in the order Bi > Pb > Sn > triethylamine > .... 46<br />
The rheological properties determined by dynamic mechanical techniques<br />
can be sensitive to the rate of mechanical deformation. The rate of<br />
expansion or possibly the rate of foam rise can be used characterizing the<br />
activity of certain catalysts.<br />
A combined measurement of the expansion <strong>and</strong> the weight loss permits<br />
characterizing the mass of CO 2 trapped within a foam, the mass of<br />
CO 2 lost, <strong>and</strong> the total mass of CO 2 generated during curing.<br />
There are three major classes of catalysts: tertiary amines, organic<br />
salts, <strong>and</strong> organometallics. Often the chemical nature of the catalysts is<br />
not disclosed in the patent literature. However, a compilation of chemical<br />
structures of commercially available catalysts useful in the manufacture of<br />
flexible foams is available. 48 Nevertheless, it is often difficult to establish<br />
structure-property relationships because of the unavailability of information.<br />
2.2.7.2 Tertiary Amine Catalysts<br />
Commercially used amines are summarized in Table 2.6 <strong>and</strong> shown in Figure<br />
2.20. Amine catalysts are often delivered as a solution in dipropylene<br />
glycol. This makes the dosage of small quantities easier.<br />
Tertiary amines are used most commonly to catalyze the urethane<br />
formation. They catalyze both gelling <strong>and</strong> blowing reactions but not the<br />
formation of isocyanurate. Tertiary amines are often formulated with organotin<br />
compounds.<br />
As the basicity increases, the crosslinking is favored. A known problem<br />
is volatility that causes odor. Further, the migration of amine catalysts<br />
can cause a discoloration when the final polyurethane is used with poly-<br />
(vinyl chloride) (PVC). This problem emerges in the automotive industry<br />
<strong>and</strong> is addressed as “vinyl staining”.<br />
The discoloration of poly(vinyl chloride) bound to polyurethane has
Polyurethanes 99<br />
Amine<br />
Table 2.6: Tertiary Amine Catalysts<br />
1,4-Diazabicyclo[2.2.2]octane (DABCO)<br />
Bis(2-dimethylaminoethyl)ether (BDMAEE)<br />
N-Ethylmorpholine<br />
N-Methylmorpholine<br />
N ′ ,N ′ -dimethylpiperazine<br />
Triethylamine<br />
N,N-dimethylethylamine<br />
Substituted pyridines<br />
2-Azabicyclo[2.2.1]heptane<br />
N-(3-Dimethylaminopropyl)-2-ethylhexanoic acid<br />
amide<br />
N,N,N ′ ,N ′ ,N ′′ -pentamethyldiethylene triamine<br />
Remarks<br />
Widely employed<br />
High-resiliency<br />
foams, heavy blowing<br />
catalyst<br />
Polyester slabstock<br />
foam<br />
Polyester slabstock<br />
foam<br />
High vapor pressure,<br />
improves skin formation<br />
in molded foam<br />
Highly volatile cure<br />
catalyst<br />
Low odor<br />
Uretdiones<br />
Heavy blowing<br />
catalyst<br />
N,N-dimethylcyclohexylamine<br />
Odorous liquid<br />
N,N-dimethylbenzylamine<br />
Polyester flexible<br />
foams<br />
N,N-Dimethylethanolamine<br />
Polyether flexible<br />
foams<br />
3-Hydroxy-1-azabicyclo[2.2.2]octane<br />
<strong>Reactive</strong> catalyst<br />
2-(2-N,N-Diethylaminoethoxy)ethanol<br />
<strong>Reactive</strong> catalyst<br />
5-Dimethylamino-3-methyl-1-pentanol<br />
<strong>Reactive</strong> catalyst, low<br />
odor 50<br />
1-(2-hydroxypropyl)imidazole<br />
<strong>Reactive</strong> catalyst<br />
1-(3 ′ -Aminopropyl)imidazole <strong>Reactive</strong> catalyst 51<br />
1-(3 ′ -(Imidazolinyl)propyl)urea<br />
51<br />
Bis(3-(N,N-dimethylamino)propyl)amine,<br />
chain-extended with polyol <strong>and</strong> polyisocyanate<br />
49<br />
52
100 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
N<br />
CH 2 CH 2<br />
CH 2 CH 2<br />
CH 2 CH 2<br />
N<br />
N<br />
CH 2 CH 3<br />
1,4-Diazabicyclo[2.2.2]octane<br />
N-Ethylmorpholine<br />
H 3 C<br />
H 3 C<br />
N<br />
CH 3<br />
CH 2 CH 2 O CH 2 CH 2 N<br />
CH 3<br />
Bis(2-dimethylaminoethyl)ether<br />
CH 2<br />
N<br />
CH3<br />
H 3 C<br />
H 3 C<br />
N<br />
CH 2 CH 2 OH<br />
2-Methyl-2-azabicyclo[2.2.1]heptane<br />
N,N-Dimethylethanolamine<br />
Figure 2.20: Tertiary Amine Catalysts: 1,4-Diazabicyclo[2.2.2]octane, N-Ethylmorpholine,<br />
Bis(2-dimethylaminoethyl)ether, 2-Azabicyclo[2.2.1]heptane, N,N-<br />
Dimethylethanolamine
Polyurethanes 101<br />
been attributed to the catalyzed dehydrochlorination of the PVC by the<br />
residual amine catalyst. 53 Amine-free catalyst systems based on carboxylates<br />
are helpful to avoid this phenomenon.<br />
54, 55<br />
The activity of amines increases with increasing basicity. However,<br />
the activity is negatively influenced by steric hindrance. The urethane<br />
formed by the reaction catalyzes further formation of urethane. Amines of<br />
the general structure RR ′ N(CH 2 ) n OR ′′ are effective blowing catalysts at<br />
n = 2, but good gelling catalysts at n = 3.<br />
Triethylene diamine is a synonym for 1,4-diazabicyclo[2.2.2]octane,<br />
which is both an excellent gelling <strong>and</strong> blowing catalyst. It is the most used<br />
tertiary amine in the production of polyurethanes. The unusual high activity<br />
of 1,4-diazabicyclo[2.2.2]octane emerges from a lack of steric hindrance<br />
in spite of its moderate basicity. Its complex with boric acid exhibits<br />
a reduced odor.<br />
Bis(2-dimethylaminoethyl)ether is used to produce high-resiliency<br />
foam, because it promotes the reaction of the isocyanate with water. It<br />
is often used together with triethylene diamine. N-ethylmorpholine <strong>and</strong> N-<br />
methylmorpholine have lower activity <strong>and</strong> are therefore used in the production<br />
of polyester slabstock foam, where only catalysts with lower activity<br />
are needed. N-Methylmorpholine, N-ethylmorpholine <strong>and</strong> triethylamine<br />
belong to the group of skin cure catalysts. These are tertiary amines with<br />
high vapor pressure. They volatilize from the developing foam to the foam<br />
mold surface, thus promoting an additional reactivity there.<br />
Substituted hexahydro-s-triazines, like 1,3,5-tris(3-dimethylaminopropyl)-s-hexahydrotriazine<br />
<strong>and</strong> hexamethylenetetramine 56 <strong>and</strong> alkylated<br />
imidazoles, like 1-methylimidazole or 1,2-dimethylimidazole 57–60 (Figure<br />
2.21) are also used in both high resiliency <strong>and</strong> rigid foams. An amidine<br />
contains a chemical structure as presented in Eq. 2.2.<br />
C N N<br />
(2.2)<br />
Certain bicyclic amidines (Fig. 2.22) exhibit a high gelling activity coupled<br />
with low volatility. However, these materials are sensitive to heat,<br />
light, <strong>and</strong> oxygen. 1,8-Diazobicyclo[5.4.0]undec-7-ene or 1,5-diazobicyclo[4.3.0]non-5-ene<br />
in combination with primary amines can catalyze the<br />
reaction of phenol blocked isocyanates. 61 The bicyclic catalyst is capa-
102 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
H 3 C<br />
N<br />
H 3 C<br />
H 2 C<br />
H 2 C<br />
H 2 C<br />
N<br />
N CH 2<br />
CH 3<br />
CH 2 CH 2 N<br />
CH 3<br />
N<br />
CH 2 CH 2 CH 2<br />
CH 3<br />
N<br />
CH 3<br />
1,3,5-Tris(3-dimethylaminopropyl)-s-hexahydrotriazine<br />
N<br />
H 2 C CH 2<br />
N N<br />
CH 2<br />
N<br />
H 2 C CH2<br />
N<br />
N<br />
CH 3<br />
Hexamethylenetetramine<br />
1-Methylimidazole<br />
Figure 2.21: 1,3,5-tris(3-dimethylaminopropyl)-s-hexahydrotriazine, hexamethylenetetramine,<br />
1-methylimidazole<br />
ble of unblocking phenol blocked isocyanate groups, <strong>and</strong> can effect curing<br />
within an hour at ambient temperature. Among the amidines the bicyclic<br />
amidines have greater activity than the monocyclic amidines. 62 Alkylamino<br />
amides, i.e. secondary amides with a pendent tertiary amine with the<br />
basic structure [(CH 3 ) 2 N(CH 2 ) 3 ] 2 NCOR are odorless <strong>and</strong> have a high resistance<br />
to hydrolysis. 63 For example, formaldehyde can be condensed<br />
with N,N-bis(3-dimethylamino-n-propyl)amine. Ammonia is evolved to<br />
yield N,N-bis[3-(dimethylamino)propyl]formamide.<br />
N<br />
N<br />
N<br />
N<br />
1,8-Diazobicyclo [5.4.0]<br />
undecene-7<br />
1,5-Diazobicyclo [4.3.0]<br />
non-5-ene<br />
Figure 2.22: 1,8-Diazobicyclo[5.4.0]undec-7-ene, 1,5-Diazobicyclo[4.3.0]non-<br />
5-ene
Polyurethanes 103<br />
These types of compounds are strong gelling catalysts. Combination<br />
of the latter compound with a weak blowing catalyst, such as methoxyethylmorpholine<br />
has been described. 64<br />
Formamide-type catalysis can be used to replace the highly volatile<br />
dimethylpiperazine. The use of N,N-Bis[3-(dimethylamino)propyl]formamide<br />
as the sole catalyst produces a tight foam. Blends with methoxyethylmorpholine<br />
or optionally with 2,2 ′ -oxybis(N,N-dimethylethanamine) are<br />
strong blowing catalysts. They improve flow, skin cure, <strong>and</strong> de-mold times<br />
in flexible molded polyether foams. 64<br />
Still less volatile catalysts can be prepared using bifunctional oxalic<br />
esters instead of formic acid derivatives. 65 This class is addressed as alkylamino<br />
oxamides. An aqueous catalyst mixture is obtained to form the salts<br />
by, e.g., salicylic acid. Alternative catalysts have cyclic structures, e.g.,<br />
bis[N-(3-imidazolidinylpropyl)]oxamide, or bis[N-(3-morpholinopropyl)]-<br />
oxamide. Headspace gas chromatography was applied to measure the fugitivity.<br />
The oxalic acid amide adducts were not volatile under the conditions<br />
of analysis.<br />
To combine good in-mold flowability <strong>and</strong> fast curing, delayed-action<br />
catalysts were developed. Reduced reactivity in reactive injection molding<br />
is sometimes desirable so that large molds could be filled completely before<br />
cure. The activity of an amine catalyst can be delayed by adding acids, such<br />
as formic acid, 2-ethylhexanoic acid, or amino acids. 66 The amine salt is<br />
less active then the free amine. As the curing proceeds the temperature<br />
rises. At elevated temperatures the amine salt dissociates to the free amine<br />
<strong>and</strong> acid.<br />
Zwitterionic salts from triethylene diamine <strong>and</strong> tetra-n-butylammonium<br />
chloroacetate also delay the reaction. The effect of controlled catalysis<br />
may be realized in improved reactivity profiles, for instance, delayed initiation<br />
or accelerated cure.<br />
67, 68<br />
A disadvantage in the usage of amine salts is the possibility of corrosion,<br />
a negative influence on the long-term properties of the final product.<br />
Half esters of diethylene glycol with maleic anhydride or phthalic<br />
anhydride can be used to neutralize, or block amines, such as bis(2-dimethylaminoethyl)ether<br />
(BDMAEE). Such types of blocked amines are<br />
noncorrosive, delayed-action catalysts for flexible foams. 69 The reaction<br />
can be performed in one stroke, allowing phthalic anhydride to react with<br />
BDMAEE in diethylene glycol.<br />
Acid-blocked amine catalysts have an unpleasant odor associated
104 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
with their use, especially when the polyurethane mixtures are cured in<br />
an oven at temperatures above 120°C. This unpleasant odor also remains<br />
in the final product, making these catalysts unsuitable for some applications.<br />
70 The incorporation of active hydrogens, such as primary <strong>and</strong> secondary<br />
hydroxyl groups <strong>and</strong> amino groups, into the catalyst structure is<br />
suitable to reduce odors <strong>and</strong> emissions.<br />
2.2.7.3 Mechanisms of Tertiary Amine Catalysts<br />
Two basic mechanisms for tertiary amine-catalyzed formation of urethane<br />
are under discussion. The first mechanism deals with the formation of<br />
an isocyanate-amine complex followed by reaction with an alcohol. This<br />
mechanism suggests that the nucleophilicity of the amine is the dominant<br />
factor. The second mechanism postulates an amine-alcohol complex that<br />
reacts with the isocyanate. According to this mechanism, the amine basicity<br />
is the dominant factor.<br />
The mechanism based on an isocyanate-amine complex seems to be<br />
more generally accepted. It is suggested that Lewis bases are activating the<br />
alcohols. 71<br />
2.2.7.4 <strong>Reactive</strong> Catalysts<br />
If the catalysts are modified with a group that reacts with isocyanates, then<br />
the catalysts can be incorporated into the polyurethane material. For example,<br />
triethanolamine has three hydroxy functions <strong>and</strong> is at the same time a<br />
tertiary amine. Other compounds include an adduct of glycidyl diethylamine<br />
with 2(di-methylamino)ethanol.<br />
72, 73<br />
A hydroxy functional tertiary amine can be produced by a Michael<br />
type reaction followed by reductive amination of the cyano group, as exemplified<br />
with 1-(3-dimethylaminopropoxy)-2-butanol in Figure 2.23. Since<br />
the butanol can attack the acrylonitrile either with the primary hydroxyl<br />
group or with the secondary hydroxyl group, in fact an isomeric mixture<br />
will be obtained. 74 In the same way an adduct with 1-methylpiperazine can<br />
be obtained.<br />
<strong>Reactive</strong> catalysts typically show a high activity in the initial stage<br />
of polymerization <strong>and</strong> then a reduced activity when they are included in<br />
the growing polymer.
Polyurethanes 105<br />
H 2 C CH C N<br />
O H<br />
CH 2 CH CH 2 CH 3<br />
OH<br />
H 2 C CH C N<br />
O H<br />
CH 2 CH CH 2<br />
OH<br />
CH 3<br />
CH 3<br />
H 2 C CH CH 2 N<br />
CH<br />
O H<br />
3<br />
CH 2 CH CH 2 CH 3<br />
OH<br />
CH 3 N CH 3<br />
+ H 2 - NH 3<br />
1-(3-Dimethylaminopropoxy)-2-butanol<br />
Figure 2.23: Synthesis of a Hydroxy Functional Tertiary Amine: 1-(3-Dimethylaminopropoxy)-2-butanol<br />
2-Dimethylaminoethyl urea or N,N ′ -Bis(3-dimethylaminopropyl)<br />
urea contains the ureido group which enables the catalysts to react into<br />
the polyurethane matrix. These reactive catalysts can be used as gelling<br />
catalysts or blowing catalysts with complementary blowing or gelling cocatalysts,<br />
respectively, which may or may not contain reactive functional<br />
groups to produce polyurethane foam materials. The reactive catalysts produce<br />
polyurethane foams which have no amine emissions. 75<br />
Examples for reactive catalysts include 3-quinuclidinol (3-hydroxy-<br />
1-azabicyclo[2.2.2]octane), 76, 77 propoxylated 3-quinuclidinol, 3-hydroxymethyl<br />
quinuclidine, 78 <strong>and</strong> 2-(2-N,N-diethylaminoethoxy)ethanol.<br />
Propoxylated 3-quinuclidinol is a liquid, which is soluble in dipropylene<br />
glycol, whereas 3-quinuclidinol is a high melting solid. 3-Methyl-3-hydroxymethyl<br />
quinuclidine may be prepared by reacting ethylpyridine<br />
with formaldehyde to afford 2-methyl-2-(4-pyridyl)-1,3-propanediol<br />
which is hydrogenated to 2-methyl-2-(4-piperidyl)-1,3-propanediol which<br />
in turn is cyclized to the quinuclidine product. 78 2-(2-N,N-diethylaminoethoxy)ethanol<br />
is superior with regard to vinyl staining.<br />
Combinations of a nonreactive catalyst <strong>and</strong> a reactive catalyst, e.g.,<br />
N,N-bis(3-dimethylaminopropyl)formamide <strong>and</strong> dimethylaminopropylurea,<br />
have been proposed for foams for interior components of automo-
106 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
biles. 79 Such low-volatility catalysts do not emit vapors over time or under<br />
the effects of heat which would otherwise cause nuisance fogging of windshields,<br />
<strong>and</strong> also reduce the chemical content of the air inside vehicles to<br />
which a driver <strong>and</strong> passengers are otherwise exposed.<br />
2.2.7.5 Anionic Catalysts<br />
Anionic catalysts favor the isocyanurate formation. Isocyanurate units are<br />
built by trimerizing an isocyanate. The isocyanurate group improves properties<br />
such as thermal resistance, flame retardancy, <strong>and</strong> chemical resistance.<br />
In quaternary ammonium carboxylates, alkali metal carboxylates<br />
<strong>and</strong> substituted phenols such as 2,4,6-tris(dimethylaminomethyl)phenol,<br />
the active species is the anion. This is different from amine salt catalysts<br />
where the active species is the free amine.<br />
Examples for quaternary ammonium carboxylates are benzylammonium<br />
carboxylate, 80 tetramethylammonium pivalate, <strong>and</strong> methyldioctyldecylammonium<br />
pivalate (C 8 H 17 ) 2 (C 10 H 21 )(CH 3 )N +− O 2 CC(CH 3 ). 81<br />
Tetraalkylammonium fluorides <strong>and</strong> cesium fluoride are extremely<br />
selective catalysts for the formation of isocyanurate. 82<br />
The trimerization of diisocyanates produces not only the trimer, i.e.,<br />
monoisocyanurate, but also higher oligomers. The viscosity of the demonomerized<br />
polyisocyanate increases as the oligomer content increases.<br />
The deactivation of the catalyst is necessary in order to terminate the<br />
trimerization <strong>and</strong> to ensure the storage stability of the polyisocyanate. The<br />
degree of trimerization can be controlled by the addition of a catalyst inhibitor.<br />
After adding the catalyst inhibitor, the trimerization stops. 83 Suitable<br />
catalyst inhibitors are compounds which enter into chemical reactions<br />
with quaternary ammonium fluorides. Examples include calcium chloride<br />
or alkyl chlorosilanes such as ethyl chlorosilane, or substances which adsorptively<br />
bind quaternary ammonium fluorides, such as silica gel. Further<br />
organic acids or acid chlorides deactivate the catalysts.<br />
Potassium octoate <strong>and</strong> tertiary phosphines are other catalysts useful<br />
for the dimerization <strong>and</strong> trimerization of isocyanates. Carboxylic acids<br />
favor the formation of urea bond compounds. 84, 85 Potassium acetate is a<br />
general purpose catalyst.<br />
2.2.7.6 Organometallic Catalysts<br />
Commonly used organometallic catalysts are shown in Table 2.7.<br />
It is
Compound<br />
Table 2.7: Organometallic Catalysts<br />
Dibutyltin dilaurate (DBTDL)<br />
Stannous octoate<br />
Dibutyltin diacetate<br />
Dibutyltin dimercaptide<br />
Lead naphthenate<br />
Lead octoate<br />
Dibutyltin bis(4-hydroxyphenylacetate)<br />
Dibutyltin bis(2,3-dihydroxypropylmercaptide)<br />
Ferric acetylacetonate<br />
Remarks<br />
Polyurethanes 107<br />
St<strong>and</strong>ard Compound<br />
Polyether-based slabstock foams<br />
Hydrolytically stable<br />
Elastomers<br />
believed that the catalytic action occurs by a ternary complex of the isocyanate,<br />
hydroxyl, <strong>and</strong> the organometallic compound. A Lewis acid-isocyanate<br />
complex is formed followed by complexation with the alcohol. 71<br />
For gelling reactions, organometallic catalysts are more selective<br />
than tertiary amines. Some organotin compounds lose their activity in the<br />
presence of water or at high temperatures. As in the case of amine catalysts,<br />
the activity decreases in sterically hindered compounds. Also, solvent<br />
effects are observed. The solvent effect is relevant for solvent-based<br />
coating formulations. Dialkyltin dimercaptides, such as dibutyltin dilauryl<br />
mercaptide, exhibit good storage times when admixed with other catalyst<br />
components. 86<br />
Dibutyltin dilaurate catalyzes the formation of urethane suppressing<br />
the formation of allophanates <strong>and</strong> isocyanurates. 87 With high resiliency<br />
foams (HR), where more reactive polyols are generally employed, very<br />
few tin catalysts can be used because the foam cell walls are less prone<br />
to rupture than with conventional foams, <strong>and</strong> this can result in shrinkage<br />
problems. 56 Bis(2-acyloxyalkyl)diorganotins exhibit only a small activity<br />
at room temperature. However they decompose at elevated temperatures<br />
into diorganotin dicarboxylates, which are the active species <strong>and</strong> olefins.<br />
For this reason they are also referred to as latent catalysts. This effect can<br />
be used to tailor catalysts. One advantage of the latent catalysts of the formula<br />
like Figure 2.24 is, therefore, to be able to mix the starting materials<br />
with the latent catalyst without catalysis of the reaction taking place <strong>and</strong><br />
to initiate the catalysis of the reaction by heating the mixture to the decomposition<br />
temperature of the latent catalyst. 2-Acetoxyethyl-dibutyltin
108 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Bu<br />
Bu<br />
Sn<br />
Cl<br />
CH 3<br />
C O<br />
O<br />
H<br />
CH<br />
CH 2<br />
hν<br />
∆<br />
Bu<br />
Bu<br />
Sn<br />
Cl<br />
CH 3<br />
C O<br />
O<br />
CH 2 CH 2<br />
Bu = CH 3<br />
CH 2<br />
CH 2<br />
CH 2<br />
Figure 2.24: Synthesis of 2-Acetoxyethyl-dibutyltin chloride from Chlorodibutyltin<br />
hydride <strong>and</strong> Vinyl acetate<br />
chloride is prepared from chlorodibutyltin hydride <strong>and</strong> vinyl acetate, c.f.<br />
Figure 2.24, <strong>and</strong> it is decomposed by heat at 90°C within one hour.<br />
88, 89<br />
Another latent tin catalyst consists of the adduct of a tin carboxylate<br />
or other tin compound with a sulfonylisocyanate, such as dibutyltin dilaurate<br />
or dibutyltin methoxide <strong>and</strong> tosyl isocyanate. 90 Tin alkoxides or tin<br />
hydroxides have a far higher catalytic activity than the tin carboxylates.<br />
These additional compounds are extremely sensitive to hydrolysis, alcoholysis<br />
<strong>and</strong> are decomposed by the presence of water.<br />
Moisture can be supplied by the substrate, the atmosphere or by<br />
compounds containing reactive groups toward isocyanate, in particular hydroxyl<br />
groups, with release of the catalysts. Before hydrolytic or alcoholytic<br />
decomposition of the addition compounds takes place, these compounds<br />
are completely inert towards isocyanate groups. They give rise to<br />
no side reactions which would impair the storage stability of organic polyisocyanates.<br />
Combinations of organotin catalysts <strong>and</strong> hydrogen chloride<br />
extend the pot-life time in coating compositions without changing the cure<br />
time. 91 Bismuth neodecanoate <strong>and</strong> combinations of bismuth <strong>and</strong> zirconium<br />
carboxylic acid salts also exhibit longer pot-life times combined with<br />
rapid curing. 92 However, catalysts based on bismuth are water sensitive<br />
<strong>and</strong> deactivate in the presence of moisture.<br />
Polymeric metal catalysts are less prone to migrate. They can be<br />
synthesized by reacting a diorganotin dichloride or dibutyltin oxide with<br />
a hydroxymercaptan, such as 3-mercapto-1,2-propanediol with water removal.<br />
A viscous polymeric material is obtained. 93<br />
Dibutyltin bis(4-hydroxyphenylacetate) <strong>and</strong> dibutyltin bis(2,3-dihydroxypropylmercaptide)<br />
are hydrolytically particularly stable. The hy-
Polyurethanes 109<br />
droxy functionality allows an incorporation in the polyurethane chain. 94<br />
A low odor <strong>and</strong> migration resistant organotin catalyst consists of<br />
the reaction products of dibutyltin oxide <strong>and</strong> aromatic aminocarboxylic<br />
acids, e.g., 3,5-diaminobenzoic acid to result in tin-di-n-butyl-di-3,5-amino<br />
benzoate. 95<br />
2.3 SPECIAL ADDITIVES<br />
Chemical formulations of polyurethane foams are based on the following<br />
ingredients:<br />
1. Polyol,<br />
2. Isocyanate,<br />
3. Catalysts,<br />
4. Water,<br />
5. Blowing agent,<br />
6. Surfactant,<br />
7. Pigment,<br />
8. Additives.<br />
2.3.1 Fillers<br />
2.3.1.1 Rectorite Nanocomposites<br />
Rectorite (REC) is a clay mineral with a 1:1 regular interstratification of<br />
a dioctahedral mica <strong>and</strong> a dioctahedral smectite. Rectorite has been used<br />
to yield intercalated or exfoliated thermoplastic polyurethane rubber nanocomposites<br />
by melt processing intercalation.<br />
X-ray diffraction <strong>and</strong> transmission electron microscopy clarified that<br />
the composites with lower amounts of clay are intercalation or part exfoliation<br />
nanocomposites. The mechanical properties of the composites are<br />
substantially enhanced. 96<br />
2.3.1.2 Zeolite<br />
Zeolite has been used for modifying the structure of polyurethane membranes<br />
<strong>and</strong> to improve their properties. Membranes with zeolite content<br />
between 10 <strong>and</strong> 70%, have been prepared. The preparation method induces<br />
an anisotropy in the membranes. The membranes have therefore an
110 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
asymmetric structure consisting of the top skin, i.e., the active layer, the<br />
substructure, <strong>and</strong> the bottom skin. 97<br />
2.3.1.3 Iron Particles<br />
The sound absorption characteristic within a certain frequency b<strong>and</strong>width<br />
of a flexible polyurethane foam can be changed, when 2 to 5 µm carbonyl<br />
iron particles are incorporated, when constant intensity magnetic fields are<br />
applied. 98<br />
2.3.2 Reinforcing Materials<br />
2.3.2.1 Nanosilica Particles<br />
Polyurethane ionomers in an aqueous emulsion were reinforced with hydrophobic<br />
nanosilica to give composites. The aqueous emulsion was stable<br />
<strong>and</strong> the particle size increased as the content of hydrophobic nanosilica was<br />
increased. The reinforcing effects of nanosilica on the mechanical properties<br />
were examined in various tests. The composites showed an enhanced<br />
thermal <strong>and</strong> water resistance. 99<br />
Nanosized SiO 2 particles can be prepared via the sol-gel process.<br />
In a sol-gel process, the inorganic mineral is formed <strong>and</strong> deposited in-situ<br />
in the organic polymer matrix, for example, aqueous emulsions of cationic<br />
polyurethane ionomers, mixed with tetraethoxysilane, hydrolyze by the action<br />
of acid. In this way, silica nanocomposites, based on poly(ε-caprolactone<br />
glycol) as soft segment, <strong>and</strong> isophorone diisocyanate as hard segment,<br />
<strong>and</strong> 3-dimethylamino-1,2-propanediol as chain extender were prepared. 100<br />
Mechanical properties are improved by the incorporation of the particles.<br />
The particles do not essentially affect the low temperature-resistant<br />
properties, but improve the heat-resistance of the resin. 101 The dispersion<br />
of the particles can be enhanced by a surface modification with (3-aminopropyl)triethoxysilane.<br />
102<br />
Polyurethane/filler composites also can be prepared by mixing the<br />
polyol with a solution of the silica in methylethylketone, then stripping<br />
the methylethylketone. This solution is then reacted with a diisocyanate,<br />
<strong>and</strong> then chain-extended with 1,4-butanediol. Atomic force microscopy<br />
revealed that the filler particles were evenly distributed in the hard <strong>and</strong> soft<br />
phases. 103
Table 2.8: Flame Retardants for Polyurethanes<br />
Compound<br />
Exp<strong>and</strong>able graphite<br />
105<br />
Triethyl phosphate<br />
106<br />
Ammonium polyphosphate<br />
107<br />
Melamine cyanurate<br />
107<br />
Poly(epichlorohydrin) (PECH)<br />
108<br />
3-Chloro-1,2-propanediol, reactive<br />
109<br />
Polyurethanes 111<br />
Reference<br />
2.3.2.2 Layered Silicate Nanocomposites<br />
High performance nanocomposites that consist of a polyurethane elastomer<br />
(PUE) <strong>and</strong> an organically modified layered silicate have been described. 104<br />
The polyurethane is based on poly(propylene glycol), 4,4 ′ -methylene bis-<br />
(cyclohexyl isocyanate) <strong>and</strong> 1,4-butanediol. The tensile strength <strong>and</strong> strain<br />
at break for these PUE nanocomposites increases more than 150%. An<br />
isocyanate index of 1.10 results in the best improvement in stress <strong>and</strong> elongation<br />
at break.<br />
Polyurethane/organophilic montmorillonite (PU/OMT) nanocomposites<br />
have an enhanced tensile strength <strong>and</strong> improved thermal properties, in<br />
comparison to unmodified polyurethane. 110 An amphiphilic urethane precursor<br />
with hydrophilic poly(ethylene oxide) (PEO) was used to prepare<br />
nanocomposites containing Na + -montmorillonite. 111<br />
2.3.2.3 Nanoclays<br />
Waterborne polyurethane/poly(methyl methacrylate) hybrid materials were<br />
reinforced with exfoliated organoclay. The size of the particles in the emulsion<br />
increased when the contents of PMMA or organoclay was increased.<br />
X-ray measurements showed an effective exfoliation of the silicate layer in<br />
the polymer matrix. 112<br />
2.3.3 Flame Retardants<br />
Flame retardants, recently described, are summarized in Table 2.8.
112 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
2.3.3.1 Poly(epichlorohydrin)<br />
Poly(epichlorohydrin) (PECH) was phosphorylated by the reaction the P-H<br />
bond of 9,10-dihydro-9-oxa-10-phosphaphenanthrene-10-oxide (DOPO)<br />
with the pendent chloromethyl groups of PECH. A phosphorus-containing<br />
PECH with hydroxyl terminal groups is thus obtained. 108 From this compound<br />
a phosphorous-containing polyurethane is obtained by the reaction<br />
with 2,4-toluene diisocyanate. The polymers are useful as multifunctional<br />
modifiers for epoxy resins <strong>and</strong> for improving the toughness <strong>and</strong> flame retardancy.<br />
2.3.3.2 Exp<strong>and</strong>able Graphite<br />
The protective shield in a polyurethane exp<strong>and</strong>able graphite (EG) system<br />
consists of exp<strong>and</strong>ed worms of graphite embedded in the tarry degraded<br />
matrix of polyurethane. 105<br />
The expansion of EG is due to a redox process between H 2 SO 4 ,<br />
intercalated between graphite layers, <strong>and</strong> the graphite itself that originates<br />
the blowing gases according to the reaction:<br />
C+2H 2 SO 4 → CO 2 + 2H 2 O+2SO 2 (2.3)<br />
Exp<strong>and</strong>able graphite can be used in poly(isocyanurate) polyurethane<br />
foams in order to improve fire behavior of such foams. In order to<br />
obtain a completely halogen-free material, water blown foams must be<br />
prepared thus avoiding the use of hydrochlorofluorocarbons or hydrofluorocarbons.<br />
The limiting oxygen index of the material without exp<strong>and</strong>able<br />
graphite is at 24% <strong>and</strong> reaches 30.5% in presence of 25% of exp<strong>and</strong>able<br />
graphite. 113 Triethyl phosphate shows a synergistic effect with exp<strong>and</strong>able<br />
graphite. 106 Further exp<strong>and</strong>able graphite or triethyl phosphate do not<br />
worsen the mechanical properties. Ammonium polyphosphate, melamine<br />
cyanurate, <strong>and</strong> exp<strong>and</strong>able graphite were tested in a comparative study.<br />
Exp<strong>and</strong>able graphite showed the best results. 107<br />
2.3.3.3 Charring Agents<br />
In the case of ammonium polyphosphate, the blowing effect is less important<br />
105 than in exp<strong>and</strong>able graphite. Ammonium polyphosphate, melamine<br />
cyanurate <strong>and</strong> exp<strong>and</strong>able graphite are compounds that form char layers<br />
that provide a thermal isolation.
Polyurethanes 113<br />
Table 2.9: Global Production/Consumption Data of Important Monomers<br />
<strong>and</strong> <strong>Polymers</strong> 115<br />
Monomer Mill. Metric tons Year Reference<br />
Phosgene 5 2002<br />
116<br />
Toluene diisocyanate 1.3 2000<br />
117<br />
p,p ′ -Methylene diphenyl diisocyanate (MDI) 2.4 2000<br />
117<br />
Ethyleneamines 0.248 2002<br />
118<br />
Phthalic anhydride 3.2 2000<br />
119<br />
Maleic anhydride 1.3 2001<br />
120<br />
1,4-Butanediol 1 2003<br />
121<br />
Polyurethane foams (flexible <strong>and</strong> semi-rigid) 2.3 2001<br />
122<br />
Polyurethane foams (rigid) 1.6 2001<br />
122<br />
Polyurethane elastomers 0.581 2001<br />
123<br />
Urethane surface coatings 1.5 1999<br />
124<br />
However, the action takes place in different ways. Ammonium polyphosphate<br />
leads to the formation of a char layer through a series of processes<br />
consisting of initial peroxide formation, decomposition to alcohols<br />
<strong>and</strong> aldehydes, formation of alkyl-phosphate esters, dehydration <strong>and</strong> subsequent<br />
char formation. 114 Thermogravimetric studies showed that the addition<br />
of ammonium polyphosphate accelerates the decomposition of the<br />
matrix but leads to an increase in the amount of high-temperature residue,<br />
under an oxidative or inert atmosphere.<br />
This stabilized residue acts as a protective thermal barrier during<br />
the intumescence fire retardancy process. The resulting char consists of<br />
an aromatic carbonaceous structure which condenses <strong>and</strong> oxidizes at high<br />
temperature. In the presence of ammonium polyphosphate, a reaction between<br />
the additive <strong>and</strong> the polymer occurs, which leads to the formation of<br />
a phosphocarbonaceous polyaromatic structure. 125<br />
Melamine cyanurate acts in an endothermic decomposition <strong>and</strong> gives<br />
off ammonia. Still nitrogen-containing polymers form then a char layer. 107<br />
2.3.4 Production Data<br />
Global Production Data of the most important monomers used for unsaturated<br />
polyurethane resins are shown in Table 2.9.
114 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
2.4 CURING<br />
The isocyanurate formation <strong>and</strong> isocyanate degree of conversion can be<br />
measured simultaneously by means of FT-IR spectroscopy. 126<br />
The curing behavior of polyurethanes based on modified methylene<br />
diphenyl diisocyanate <strong>and</strong> poly(propylene oxide) polyols has been studied<br />
using isothermal Fourier-transform infrared (FTIR) spectroscopy , differential<br />
scanning calorimetry (DSC) <strong>and</strong> adiabatic exothermic experiments.<br />
Increasing the concentration of the catalyst, i.e., dibutyltin dilaurate<br />
(DBTDL) or decreasing the molecular weight of the polyol raises the<br />
rate of reaction <strong>and</strong> shifts the DSC exothermic peak temperature to lower<br />
temperatures.<br />
However, the heat of reaction remains constant. A marked increase<br />
in reaction rate is observed when an ethylene oxide end-capped polyol<br />
is used instead of a st<strong>and</strong>ard propylene oxide end-capped polyol. The<br />
conversion of isocyanate for several concentrations of dibutyltin dilaurate<br />
(DBTDL) fits a second-order kinetics. The activation energy of curing is<br />
independent of the molecular weight of the hydroxy compound. 127 However,<br />
the activation energy depends on the extent of conversion. 47<br />
With isocyanate reactive hot-melt adhesives an autocatalytic effect<br />
was observed. The autocatalysis is not dependent on the structure of diols<br />
but on the isocyanates. 128<br />
2.4.1 Recycling<br />
2.4.1.1 Solvolysis<br />
In recycling, catalysts can effect a reduction of the time required to recycle<br />
polyurethanes via hydrolysis <strong>and</strong> glycolysis. The products of polyurethane<br />
recycling are a complex mixture of alcohols <strong>and</strong> amines. Useful catalysts<br />
for recycling include titanium tetrabutoxide, potassium acetate, sodium hydroxide<br />
or lithium hydroxide. uncatalyzed polyurethane recycling is also<br />
possible.<br />
The recovery <strong>and</strong> purification of the polyol-containing liquid products<br />
can be achieved by the distillation of the glycolysis products. The<br />
amount of recoverable products by distillation reaches a maximum of 45%,<br />
when a process temperature of 245 to 260°C is applied. 129
Polyurethanes 115<br />
2.4.1.2 Ultrasonic Reactor<br />
High resiliency polyurethane foam has been recycled by the application of<br />
high-power ultrasound in a continuous ultrasonic reactor. The foam has<br />
been decrosslinked at various screw speeds <strong>and</strong> various ultrasound amplitudes,<br />
then blended at different ratios with the virgin polyurethane rubber<br />
<strong>and</strong> then cured. In comparison to the ground recycled samples, the blends<br />
of the decrosslinked samples are easier to mix <strong>and</strong> exhibit enhanced properties.<br />
130<br />
2.4.1.3 Polyacetal-modified Polyurethanes<br />
Polyacetals are thermally stable but undergo a degradation by treatment<br />
with aqueous acid even at room temperature. Therefore, polyacetals are<br />
c<strong>and</strong>idates for degradable polymers for chemical recycling. Polyurethane<br />
elastomers with degradable polyacetal soft segments have been synthesized.<br />
131 The polyurethanes were synthesized from polyacetal glycol <strong>and</strong><br />
4,4-diphenylmethane diisocyanate. 1,4-Butanediol was used as a chain<br />
extender. For comparison, samples containing a polyether glycol instead<br />
of the polyacetal glycol were prepared. Acid treatment indicated that the<br />
degradation took place.<br />
2.4.1.4 Production Wastes<br />
Waste residue from the production of toluene diisocyanate was used as a<br />
modifier in making improved waterproofing bitumen. The degree of improvement<br />
of the softening point could be correlated with the blend morphology.<br />
132<br />
2.5 PROPERTIES<br />
2.5.1 Mechanical Properties<br />
Copolymers of propylene oxide <strong>and</strong> ethylene oxide are used for softer<br />
foams in comparison with polyols obtained exclusively from propylene<br />
oxide.<br />
In comparison with polyether polyurethanes, polyester polyurethanes<br />
are more resistant to oil, grease, solvents, <strong>and</strong> oxidation. They exhibit<br />
better mechanical properties. On the other h<strong>and</strong>, polyester polyurethanes<br />
are less chemically stable <strong>and</strong> are also sensitive to microbiological attack.
116 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
2.5.2 Thermal Properties<br />
Additives, in particular nanocomposites, have a positive effect on the thermal<br />
properties. On heating up to degradation, the urethane structure undergoes<br />
a retro reaction into isocyanates. Therefore, highly poisonous products<br />
can be formed. The isocyanates yield depends greatly on the specific<br />
combustion conditions selected, such as temperature, ventilation, <strong>and</strong> fuel<br />
load.<br />
The mechanism of thermal degradation has been sketched. 133 Polyurethane<br />
undergoes a depolycondensation. Volatile diisocyanate <strong>and</strong> isocyanate-terminated<br />
fragments are formed. 134<br />
In laboratory combustion experiments, isocyanates could be detected<br />
in the gaseous effluent. They were analyzed using impinger flasks containing<br />
1-(2-methoxyphenyl)piperazine (MOPIP) as derivatizing reagent. The<br />
derivatives were analyzed by high performance liquid chromatography <strong>and</strong><br />
t<strong>and</strong>em mass spectrometry. Isocyanic acid, aliphatic isocyanates, alkenyl<br />
isocyanates, <strong>and</strong> other derivatives were found. 135<br />
Heavy metals influence the thermal degradation. Manganese, cobalt,<br />
<strong>and</strong> iron ions favor the polyurethane degradation. Chromium <strong>and</strong> copper<br />
ions reduce the initial thermal stability of the polyurethane <strong>and</strong> have a<br />
catalytic effect on the second stage of its decomposition, but enhance the<br />
thermal stability of its intermediate decomposition products. By the modification<br />
of polyurethanes with these transition metal ions, changes in the<br />
decomposition mechanism of the polyurethane are induced. 136<br />
2.5.3 Weathering Resistance<br />
In aliphatic polyurethane-acrylate (PUA) resins, usually used for coatings,<br />
the urethane linkage is the most sensitive bond type with respect to photodegradation.<br />
The materials exhibit good weathering properties. 137<br />
2.6 APPLICATIONS AND USES<br />
2.6.1 Casting<br />
Cold casting <strong>and</strong> hot casting systems are available. A polyurethane/poly-<br />
(styrene-co-divinylbenzene) system can be cured at room temperature, in<br />
a one-step process. 138
Table 2.10: Interpenetrating Polymer Networks<br />
Polyurethanes 117<br />
Polyurethane Further Component Reference<br />
Castor oil-based<br />
polyurethane<br />
Poly(acrylonitrile),<br />
unsaturated polyester resin<br />
Polyurethane– Poly(acrylonitrile)<br />
140<br />
poly(ethylene oxide)<br />
Polyurethane Vinylester resin<br />
141<br />
Polyurethane Poly(styrene)<br />
142<br />
Polyurethane ionomer Poly(vinyl chloride)<br />
143<br />
Polyurethane Poly(acrylate) latex<br />
144, 145<br />
Polyurethane Poly(methacrylate)<br />
146–148<br />
Polyurethane Poly(butyl methacrylate)<br />
149<br />
Polyurethane Poly(acrylamide)<br />
150<br />
Polyurethane Nitrokonjac glucomannan<br />
151<br />
Polyurethane Epoxy resin<br />
152, 153<br />
Polyurethane Poly(vinylpyrrolidone)<br />
154<br />
Polyurethane Poly(benzoxazine)<br />
155<br />
Polyurethane Poly(allyl diglycol carbonate)<br />
156<br />
139<br />
2.7 SPECIAL FORMULATIONS<br />
2.7.1 Interpenetrating Networks<br />
Several types of interpenetrating networks with polyurethanes have been<br />
prepared <strong>and</strong> characterized. These types are summarized in Table 2.10.<br />
In a tricomponent interpenetrating polymer network composed of<br />
castor oil, toluene diisocyanate, acrylonitrile, ethylene glycol diacrylate,<br />
<strong>and</strong> an unsaturated polyester resin, it was found that the tensile strength of<br />
the unsaturated polyester (UP) matrix was decreased <strong>and</strong> flexural <strong>and</strong> impact<br />
strengths were increased upon incorporating polyurethane/polyacrylonitrile<br />
(PU/PAN) networks. 139<br />
Poly(methyl methacrylate-co-2-methacryloyloxyethyl isocyanate) can<br />
be crosslinked with various diols that result in polyurethane structures. The<br />
crosslinking kinetics of diols, such as ethylene glycol (EG), 1,6-hexanediol,<br />
<strong>and</strong> 1,10-decanediol (DD) has been investigated, <strong>and</strong> second-order<br />
kinetics was observed. The rate constants decreased from EG to DD. 146<br />
The addition of nanosized silicon dioxide can improve compatibility,<br />
damping <strong>and</strong> phase structure of interpenetrating networks. 152
118 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
CH 2 OH<br />
CH 2 OH<br />
O<br />
O<br />
OH<br />
O<br />
OH<br />
O<br />
NH 2<br />
n<br />
H 3 C CH 2 N C O<br />
CH 3<br />
H 3 C<br />
NH<br />
C O<br />
NH<br />
CH 2<br />
CH 3<br />
n<br />
O<br />
C<br />
N<br />
CH 3<br />
O<br />
C<br />
N<br />
CH 3<br />
Figure 2.25: Reaction of Chitosan with Isophorone<br />
2.7.2 Grafting with Isocyanates<br />
2.7.2.1 Chitosan<br />
Chitosan is a linear polysaccharide obtained from the N-deacetylation of<br />
chitin. The amino group in chitosan can be reacted with an isocyanate,<br />
as shown in Figure 2.25, exemplified with isophorone diisocyanate. If in<br />
addition a polyol is present, then the second isocyanate group in isophorone<br />
can react with the polyol <strong>and</strong> longer pendent polyurethane chains can be<br />
formed. 157<br />
2.7.3 Medical <strong>Applications</strong><br />
2.7.3.1 Siloxane-based Polyurethanes<br />
Polyurethane elastomers are used for medical implants. Deficiencies of<br />
conventional polyurethanes include deterioration of mechanical properties<br />
<strong>and</strong> degradation by hydrolysis reactions. Polyurethanes with improved<br />
long-term biostability are based on polyethers, hydrocarbons, poly(carbonate)s,<br />
<strong>and</strong> siloxane macrodiols. These components are intended to replace<br />
the conventional polyesters <strong>and</strong> polyethers. Siloxane-based polyurethanes<br />
show excellent biostability. 158
Polyurethanes 119<br />
2.7.3.2 Blood Compatibility<br />
Polyurethanes are widely used as blood-contacting biomaterials because<br />
they exhibit good biocompatibility <strong>and</strong> further due to their mechanical<br />
properties. However, the blood compatibility is not adequate for certain<br />
applications. Modification of the surface is an effective way to improve<br />
the blood compatibility.<br />
Sulfonic <strong>and</strong> carboxyl groups can effectively improve the blood compatibility<br />
of polyurethane. Films of polyurethane containing acrylic acid<br />
were exposed to a sulfur dioxide plasma to graft sulfonic acid group on its<br />
surfaces. During the preparation of the films by dissolution, acrylic acid<br />
polymerizes to some extent. 159<br />
Carboxybetaine has been grafted onto polyurethane. A three-step<br />
procedure was used. First, the film surfaces were treated with hexamethylene<br />
diisocyanate in presence of DBTDL. Then, N,N-dimethylethylethanolamine<br />
(DMEA) or 4-dimethylamino-1-butanol (DMBA), respectively,<br />
was allowed to react in toluene with the pendent isocyanate groups. Finally,<br />
carboxybetaines were formed in the surface by ring opening involving<br />
the tertiary amine of DMEA or DMBA <strong>and</strong> β-propiolactone (PL). 160<br />
Similarly, sulfobetaines can be formed on the surface by the reaction of<br />
1,3-propanesulfone (PS) instead of PL.<br />
161, 162<br />
A polyurethane containing a phosphorylcholine structure has improved<br />
blood compatibility. The phosphorylcholine moiety consists of<br />
(6-hydroxy)hexyl-2-(trimethylaminonio)ethyl phosphate (HTEP). A segmented<br />
polyurethane (SPU) containing the phosphorylcholine structure<br />
was synthesized from diphenylmethane diisocyanate, soft segment polytetramethylene<br />
glycol (PTMG), <strong>and</strong> HTEP, with 1,4-butanediol (BD) as a<br />
chain extender. 163 The phosphorylcholine structure on the surface of the<br />
SPU was proven by attenuated total reflectance Fourier transform infrared<br />
spectroscopy (ATR-FTIR), X-ray photoelectron spectroscopy (XPS) <strong>and</strong><br />
water contact angle measurements.<br />
2.7.3.3 Degradable Polyurethanes<br />
Longitudinal lesions in the meniscus are frequent orthopedic problems of<br />
the knee. The repair by simple techniques is limited to the vascular part<br />
of the meniscus. For the repair of the avascular part of the meniscus, a<br />
scaffold consisting of polyurethane foam has been developed. The scaffold<br />
is intended to assist the body in the formation of new meniscus cell tissue.
120 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
A segmented polyurethane with poly(ε-caprolactone) as the soft segment<br />
<strong>and</strong> 1,4-butanediisocyanate <strong>and</strong> 1,4-butanediol as uniform hard segments<br />
was chosen. 164 The material has a micro phase separated morphology<br />
<strong>and</strong> excellent mechanical properties. Foams were prepared for a porous<br />
scaffold. The scaffold was tested by implantation in the knees of beagles.<br />
It was found that meniscus-like tissue had been formed in the scaffold.<br />
Another biodegradable, sponge-like polyurethane scaffold consists<br />
of lysine-diisocyanate (LDI) <strong>and</strong> glycerol. Ascorbic acid (AA) was copolymerized<br />
with LDI-glycerol. 20<br />
The cytocompatibility of polyurethane porous scaffolds is improved<br />
by photo grafting of methacrylic acid or poly(2-hydroxyethyl acrylate)<br />
onto the surface.<br />
165, 166<br />
Polyurethanes can be degraded by esterase. This may contribute<br />
to the failure of medical implants. A strong dependence on the enzyme<br />
concentration for polyurethanes with different hard segment chemistry was<br />
established. 167<br />
2.7.3.4 Prevention of Polyurethane Heart Valve Cusp Calcification<br />
The calcification of polyurethane prosthetic heart valve leaflets is highly<br />
undesirable. Polyurethane valves modified with covalently linked bisphosphonate<br />
groups are resistant to calcification, but the highly polar bisphosphonate<br />
groups on the polyurethane surface attract sodium counter ion,<br />
therefore, water absorption is increased. However, attaching diethylamino<br />
groups to the bisphosphonate-modified polyurethane will reduce water<br />
absorption. 168<br />
2.7.4 Waterborne Polyurethanes<br />
Waterborne polyurethanes are used mainly for coatings, but also for composites<br />
<strong>and</strong> nanocomposites. They are covered briefly, with special attention<br />
to their chemistry. Water dispersable paints can be produced from<br />
polyester polyol, isophorone diisocyanate <strong>and</strong> hydrophilic monomers such<br />
as dimethylol propionic acid (DMPA) <strong>and</strong> tartaric acid (TA). 169 Phosphorus-containing<br />
flame retardant water-dispersed polyurethane coatings<br />
were also synthesized by incorporating a phosphorus compound into the<br />
polyurethane main chain. 170
Polyurethanes 121<br />
Table 2.11: Composites Made From Waterborne Polyurethane Materials<br />
Second Compound<br />
Reference<br />
Starch<br />
174<br />
Carboxymethyl konjac glucomannan (CMKGM)<br />
175<br />
Casein<br />
176<br />
Carboxymethyl chitin<br />
177, 178<br />
Soy flour<br />
179<br />
Bis(4-aminophenyl)phenylphosphine oxide (BAPPO) was obtained<br />
from bis(4-nitrophenyl)phenylphosphine oxide by the reduction of the nitro<br />
groups. 171<br />
The stability of waterborne dispersions can be improved by using a<br />
continuous process of preparation. 172 Acetone addition has a large effect<br />
on the particle diameter. 173<br />
Waterborne anionomeric polyurethane-ureas can be made from dimethylol<br />
terminated perfluoropolyethers, isophorone diisocyanate, dimethylol<br />
propionic acid, <strong>and</strong> ethylene diamine. The materials are obtained as<br />
stable aqueous dispersions.<br />
Surface properties <strong>and</strong> chemical resistance were estimated by the<br />
measurement of contact angles <strong>and</strong> spot tests with different solvents. The<br />
surface hydrophobicity was not affected by the composition. Water-sorption<br />
behavior is however sensitive to the content of carboxyl groups in the<br />
polymer. 180<br />
Another type of waterborne polyurethane-urea anionomers consists<br />
of isophorone diisocyanate, poly(tetramethylene ether) glycol, dimethylol<br />
butanoic acid (DMBA), <strong>and</strong> hydrazine monohydrate (HD). Ethylene diamine<br />
(EDA), 1,4-butane diamine (BDA) are chain extenders. The pendent<br />
carboxylic groups are neutralized by ammonia/copper hydroxyde or<br />
triethylamine (TEA). 181<br />
Table 2.11 summarizes composites made from waterborne polyurethane<br />
materials. Composite materials were prepared by blending carboxymethyl<br />
konjac glucomannan (CMKGM) <strong>and</strong> a waterborne polyurethane<br />
(WPU). A blend sheet with 80% CMKGM exhibited good miscibility <strong>and</strong><br />
higher tensile strength (89.1 MPa) than that of both of the individual materials,<br />
i.e. waterborne polyurethane sheets (3.2 MPa) <strong>and</strong> CMKGM (56.4<br />
MPa) sheets. With an increase of CMKGM content, the tensile strength,<br />
Young’s modulus, <strong>and</strong> thermal stability increased significantly, attributed
122 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
to intermolecular hydrogen-bonding between CMKGM <strong>and</strong> WPU. 175<br />
Waterborne polyurethane <strong>and</strong> casein have been prepared by blending<br />
at 90°C for 30 min, <strong>and</strong> then crosslinking with ethanedial. Water resistance<br />
of the materials proved to be quite good. 176<br />
2.7.5 Ceramic Foams<br />
Organic polymers can be used in the manufacture of ceramic components.<br />
The organic polymers are admixed with the inorganic ceramic components,<br />
either to ceramic powder or to an inorganic monomer, as processing aids.<br />
Such a mixture can be processed in injection molding machines or by other<br />
techniques. The organic polymer supports the process of shaping a green<br />
part. Subsequently it is volatilized by pyrolysis or oxidation during heating.<br />
Ceramic foams can be produced with polyurethane <strong>and</strong> ceramic powder<br />
mixtures. 182<br />
2.7.6 Adhesion Modification<br />
In order to increase the compatibility between polyamide 6 <strong>and</strong> thermoplastic<br />
polyurethane, the polyurethane was reactively modified. 183<br />
2.7.7 Electrolytes<br />
Polymer electrolytes are used as solid electrolyte materials in rechargeable<br />
lithium batteries <strong>and</strong> electrochromic devices.<br />
Solid polymer electrolytes (SPE) have been introduced since the discovery<br />
of poly(ethylene oxide)electrolytes. 184–186<br />
In polyethers, the dissociation of alkali-metal salts occurs by the formation<br />
of transient crosslinks between the ether oxygen groups in the host<br />
polymer <strong>and</strong> alkali-metal cations. The anion is usually not solvated. The<br />
main deficiency of polyether-type electrolytes is the high degree of crystallization<br />
of the polyether.<br />
Thermoplastic polyether polyurethanes (TPU), doped with various<br />
alkali metal salts, have also been studied as polymer electrolytes. TPU<br />
exhibits good mechanical properties, a tough crystallinity of the polyether<br />
segments is reduced.<br />
Polyurethanes can be modified with chelate groups in order to enhance<br />
the electrical properties. ((3-(4-(1-(4-(3-(Bis-carboxymethylamino)<br />
2-hydroxy-propoxy) phenyl)-1-methyl-ethyl) phenoxy) 2-hydroxypropyl)
Polyurethanes 123<br />
HO<br />
CH 3<br />
CH 2 O<br />
C<br />
O CH 2<br />
CH<br />
CH 3<br />
CH<br />
OH<br />
CH 2 CH 2<br />
N<br />
N<br />
H 2 C CH 2<br />
H 2 C CH 2<br />
O C C O<br />
O C C O<br />
HO<br />
OH<br />
Figure 2.26: ((3-(4-(1-(4-(3-(Bis-carboxymethylamino) 2-hydroxy-propoxy)<br />
phenyl)-1-methyl-ethyl) phenoxy) 2-hydroxypropyl) carboxy methylamino) acetic<br />
acid<br />
HO<br />
OH<br />
carboxy methylamino) acetic acid (EPIDA), c.f. Figure 2.26, is such a<br />
chelate. The molecule bears hydroxyl functions, which are basically reactive<br />
with isocyanate groups. Therefore, it can be built into a polyurethane<br />
chain. 187 These electrolytes, due to the chelating groups, exhibit a significant<br />
interaction of the Li + ions. A change in polymer morphology is<br />
also observed. An increase in the glass transition temperature of the soft<br />
segment occurs.<br />
Porous polymers, based on polyurethane/polyacrylate, can be prepared<br />
by emulsion polymerization. During the production, no organic solvent<br />
is used. The synthesis proceeds in four steps, listed here. 188<br />
1. A prepolymer is prepared from 2,4-toluene diisocyanate <strong>and</strong> poly-<br />
(propylene glycol). 2,4-toluene diisocyanate is in a two-fold excess.<br />
2. 2-Hydroxyethyl methacrylate (HEMA) is added to the prepolymer.<br />
The hydroxyl groups react with the residual isocyanate groups.<br />
3. Again poly(ethylene glycol) is added in order to react with the remaining<br />
isocyanate groups. A macromonomer with pendant double<br />
bonds is obtained.<br />
4. The macromonomer is emulsified <strong>and</strong> polymerized by the addition<br />
of 2,2 ′ -azobis(isobutyronitrile).<br />
The ionic conductivity is about 10 −3 Scm −1 at room temperature.<br />
This conductivity is useful for many practical electrochemical applications.<br />
A light-emitting electrochemical cell (LEC) is composed of a blend
124 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
of semiconducting polymer <strong>and</strong> polymer electrolyte mixture.<br />
An electrochemical cell was built from poly(p-phenylene vinylene)<br />
(PPV), as light-emitting material <strong>and</strong> lithium ion conducting waterborne<br />
polyurethane ionomer as solid electrolyte. 189 The polyurethane was prepared<br />
from a poly(ethylene glycol), α,α ′ -dimethylol propionic acid <strong>and</strong><br />
isophorone diisocyanate.<br />
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142. T. T. Alekseeva, S. I. Grishchuk, Y. S. Lipatov, N. V. Babkina, <strong>and</strong> N. V.<br />
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143. S. N. Jaisankar, Y. Lakshminarayana, <strong>and</strong> G. Radhakrishnan. Semi-interpenetrating<br />
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144. S. Chen <strong>and</strong> L. Chen. Structure <strong>and</strong> properties of polyurethane/polyacrylate<br />
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145. L. Chen <strong>and</strong> S. Chen. Latex interpenetrating networks based on polyurethane,<br />
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146. T. Kiguchi, H. Aota, <strong>and</strong> A. Matsumoto. Crosslinking polymerization<br />
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147. J. Culin, Z. Veksli, A. Anzlovar, <strong>and</strong> M. Zigon. Spin probe study of semi-interpenetrating<br />
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150. S. H. Baek <strong>and</strong> B. K. Kim. Synthesis of polyacrylamide/polyurethane hydrogels<br />
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151. S. J. Gao, L. N. Zhang, <strong>and</strong> Q. L. Huang. Effect of the synthesis route on the<br />
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152. H. W. Zhang, B. Wang, H. T. Li, Y. Jiang, <strong>and</strong> J. Y. Wang. Synthesis<br />
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September 2003.<br />
153. C. N. Cascaval, D. Rosu, L. Rosu, <strong>and</strong> C. Ciobanu. Thermal degradation of<br />
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154. L. V. Karabanova, G. Boiteux, O. Gain, G. Seytre, L. M. Sergeeva, E. D.<br />
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155. Y. J. Cui, Y. Chen, X. L. Wang, G. H. Tian, <strong>and</strong> X. Z. Tang. Synthesis<br />
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polymer networks (IPNs). Polym. Int., 52(8):1246–1248, August 2003.<br />
156. S. Dadbin <strong>and</strong> M. Frounchi. Effects of polyurethane soft segment <strong>and</strong> crosslink<br />
density on the morphology <strong>and</strong> mechanical properties of polyurethane/-<br />
poly(allyl diglycol carbonate) simultaneous interpenetrating polymer networks.<br />
J. Appl. Polym. Sci., 89(6):1583–1595, August 2003.<br />
157. S. S. Silva, S. M. C. Menezes, <strong>and</strong> R. B. Garcia. Synthesis <strong>and</strong> characterization<br />
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2003.<br />
158. P. A. Gunatillake, D. J. Martin, G. F. Meijs, S. J. McCarthy, <strong>and</strong> R. Adhikari.<br />
Designing biostable polyurethane elastomers for biomedical implants. Aust.<br />
J. Chem., 56(6):545–557, 2003.<br />
159. Q. Lv, C. B. Cao, <strong>and</strong> H. S. Zhu. Blood compatibility of polyurethane<br />
immobilized with acrylic acid <strong>and</strong> plasma grafting sulfonic acid. J. Mater.<br />
Sci. -Mater. Med., 15(5):607–611, May 2004.<br />
160. Y. Jiang, J. Zhang, J. Zhou, Y.-L. Yuan, J. Shen, <strong>and</strong> L. Si-cong. Platelet adhesion<br />
onto segmented polyurethane surfaces modified by carboxybetaine.<br />
J. Biomater. Sci., Polym. Ed., 14(12):1339–1349, 2003.<br />
161. Y. Jiang, Y.-L. Yuan, J. Shen, S. cong Lin, W. Zhu, <strong>and</strong> J. lin Fang. Grafting<br />
of sulfobetaine onto a polyurethane surface to improve blood compatibility.<br />
Chin. J. Polym. Sci., 21(4):419–425, July 2003.<br />
162. Y. Jiang, B. Rongbing, T. Ling, S. Jian, <strong>and</strong> L. Si-Cong. Blood compatibility<br />
of polyurethane surface grafted copolymerization with sulfobetaine<br />
monomer. Colloids <strong>and</strong> Surfaces B: Biointerfaces, 36(1):27–33, July 2004.
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163. L. Chen, L. Wang, Z. M. Yang, J. Shen, <strong>and</strong> S. C. Lin. Synthetic studies on<br />
blood compatible biomaterials 13: A novel segmented polyurethane containing<br />
phosphorylcholine structure: Synthesis, characterization <strong>and</strong> blood<br />
compatibility evaluation. Chin. J. Polym. Sci., 21(1):45–50, January 2003.<br />
164. R. G. J. C. Heijkants, R. V. Van Calck, J. H. De Groot, A. J. Pennings, A. J.<br />
Schouten, T. G. Van Tienen, N. Ramrattan, P. Buma, <strong>and</strong> R. P. H. Veth.<br />
Design, synthesis <strong>and</strong> properties of a degradable polyurethane scaffold for<br />
meniscus regeneration. J. Mater. Sci. -Mater. Med., 15(4):423–427, April<br />
2004. Special Issue: Selected papers from the 18th European Conference<br />
on Biomaterials (ESB2003), Stuttgart, Germany, 2003.<br />
165. C. Y. Gao, X. H. Hu, Y. Hong, J. J. Guan, <strong>and</strong> J. C. Shen. Photografting of<br />
poly(hydroxylethyl acrylate) onto porous polyurethane scaffolds to improve<br />
their endothelial cell compatibility. J. Biomater. Sci., Polym. Ed., 14(9):<br />
937–950, 2003.<br />
166. Y. B. Zhu, C. Y. Gao, J. J. Guan, <strong>and</strong> J. C. Shen. Engineering porous polyurethane<br />
scaffolds by photografting polymerization of methacrylic acid for<br />
improved endothelial cell compatibility. J. Biomed. Mater. Res., Part A,<br />
67A(4):1367–1373, December 2003.<br />
167. Y. W. Tang, R. S. Labow, <strong>and</strong> J. P. Santerre. Enzyme induced biodegradation<br />
of polycarbonate-polyurethanes: dose dependence effect of cholesterol<br />
esterase. Biomaterials, 24(12):2003–2011, May 2003.<br />
168. I. Alferiev, S. J. Stachelek, Z. B. Lu, A. L. Fu, T. L. Sellaro, J. M. Connolly,<br />
R. W. Bianco, M. S. Sacks, <strong>and</strong> R. J. Levy. Prevention of polyurethane<br />
valve cusp calcification with covalently attached bisphosphonate diethylamino<br />
moieties. J. Biomed. Mater. Res., Part A, 66A(2):385–395, August<br />
2003.<br />
169. G. Gunduz <strong>and</strong> R. R. Kisakijrek. Structure-property study of waterborne<br />
polyurethane coatings with different hydrophilic contents <strong>and</strong> polyols. J.<br />
Dispersion Sci. Technol., 25(2):217–228, March 2004.<br />
170. F. Celebi, L. Aras, G. Gunduz, <strong>and</strong> I. M. Akhmedov. Synthesis <strong>and</strong> characterization<br />
of waterborne <strong>and</strong> phosphorus-containing flame retardant polyurethane<br />
coatings. J. Coat. Technol., 75(944):65–71, September 2003.<br />
171. F. Celebi, O. Polat, L. Aras, G. Gunduz, <strong>and</strong> I. M. Akhmedov. Synthesis<br />
<strong>and</strong> characterization of water-dispersed flame-retardant polyurethane resin<br />
using phosphorus-containing chain extender. J. Appl. Polym. Sci., 91(2):<br />
1314–1321, January 2004.<br />
172. M. Keyvani. Improved polyurethane dispersion stability via continuous process.<br />
Adv. Polym. Technol., 22(3):218–224, Fall 2003.<br />
173. C. Chinwanitcharoen, S. Kanoh, T. Yamada, S. Hayashi, <strong>and</strong> S. Sugano.<br />
Preparation of aqueous dispersible polyurethane: Effect of acetone on the<br />
particle size <strong>and</strong> storage stability of polyurethane emulsion. J. Appl. Polym.<br />
Sci., 91(6):3455–3461, March 2004.
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Appl. Polym. Sci., 90(12):3325–3332, December 2003.<br />
175. G. Yang, Q. Huang, L. Zhang, J. Zhou, <strong>and</strong> S. Gao. Miscibility <strong>and</strong> properties<br />
of blend materials from waterborne polyurethane <strong>and</strong> carboxymethyl<br />
konjac glucomannan. J. Appl. Polym. Sci., 92(1):77–83, April 2004.<br />
176. N. G. Wang, L. Zhang, Y. S. Lu, <strong>and</strong> Y. M. Du. Properties of crosslinked<br />
casein/waterborne polyurethane composites. J. Appl. Polym. Sci., 91(1):<br />
332–338, January 2004.<br />
177. M. Zeng, L. N. Zhang, N. G. Wang, <strong>and</strong> Z. C. Zhu. Miscibility <strong>and</strong> properties<br />
of blend membrane of waterborne polyurethane <strong>and</strong> carboxymethylchitin.<br />
J. Appl. Polym. Sci., 90(5):1233–1241, October 2003.<br />
178. M. Zeng, L. Zhang, <strong>and</strong> Y. Zhou. Effects of solid substrate on structure <strong>and</strong><br />
properties of casting waterborne polyurethane/carboxymethylchitin films.<br />
Polymer, 45(10):3535–3545, May 2004.<br />
179. Y. Chen, L. N. Zhang, <strong>and</strong> L. B. Du. Structure <strong>and</strong> properties of composites<br />
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180. S. Turri, M. Levi, <strong>and</strong> T. Trombetta. Waterborne anionomeric polyurethane-ureas<br />
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3<br />
Epoxy Resins<br />
Epoxy resins are formed from an oligomer containing at least two epoxide<br />
groups <strong>and</strong> a curing agent, usually either an amine compound or a diacid<br />
compound. A great variety of such resins is on the market. There are many<br />
monographs on epoxy resins available. 1, 2<br />
3.1 HISTORY<br />
N. Prileschajew discovered in 1909 that olefins can react with peroxybenzoic<br />
acid to epoxides. 3 Schlack claimed in 1939 a polymeric material based<br />
on amines <strong>and</strong> multi functional epoxides. 4 Castan ∗ , in the course of searching<br />
for dental materials claimed the preparation of bisphenol A diglycidyl<br />
ether (DGEBA). 5, 6 A similar material, but higher in molecular weight,<br />
was invented by S. O. Greenlee. 7 Epoxy resins came on the market around<br />
1947. The first major intended application was as coating material.<br />
3.2 MONOMERS<br />
3.2.1 Epoxides<br />
Epichlorohydrin is the monomer used for the synthesis of glycidyl ethers<br />
<strong>and</strong> glycidyl esters. Epichlorohydrin (1-chloro-2,3-epoxypropane) is synthesized<br />
from propene via allyl chloride. A number of epoxides are shown<br />
∗ Pierre Castan, born in Bern 1899, died in Geneva 1985<br />
139
140 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
O<br />
CH 2 O C<br />
CH 3 H 3 C<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
Figure 3.1: Cycloaliphatic Epoxides<br />
in Table 3.1. <strong>Reactive</strong> diluents, i.e. monofunctional epoxide compounds<br />
are shown in Table 3.2. The curing of cycloaliphatic epoxides proceeds<br />
easily with anhydrides, but is too slow with amines. Synthetic procedures<br />
for including styrenic, cinnamoyl, or maleimide functionalities, into cycloaliphatic<br />
epoxy compounds, have been described. 8<br />
3.2.1.1 Epoxide Equivalent Weight<br />
The equivalent weight of the epoxide used is an important parameter for<br />
the amount of curing agent needed. The common method to determine the<br />
equivalent weight is the titration procedure with HBr in glacial acetic acid.<br />
However, a method for the determination of the epoxide equivalent weight<br />
in liquid epoxy resins using proton nuclear magnetic resonance ( 1 H-NMR)<br />
spectroscopy has been described. 9<br />
3.2.2 Phenols<br />
Bisphenol A is the most important ingredient in st<strong>and</strong>ard epoxy resins. It is<br />
prepared by the condensation of acetone with phenol. The latter two compounds<br />
can be prepared in the Hock process by the oxidation of cumene.<br />
Phenolic products are shown among others in Table 3.3 <strong>and</strong> Figure<br />
3.2. The hydroxyl <strong>and</strong> amino functions are epoxidized with epichlorohydrin.
Epoxide<br />
Epichlorohydrin<br />
Butadiene diepoxide<br />
1,4-butanediol diglycidyl ether<br />
(1,4-BDE)<br />
Glycerol diglycidyl ether<br />
1,3-Didodecyloxy-2-glycidylglycerol<br />
Table 3.1: Epoxides<br />
Remark/Reference<br />
Epoxy Resins 141<br />
Used for the formation of glycidyl<br />
ethers <strong>and</strong> esters<br />
10<br />
Amphiphilic polymers, for potential<br />
use as emulsifiers <strong>and</strong> solubilizing<br />
agents 11<br />
Poly(butadiene) epoxides<br />
Flexible<br />
Vinylcyclohexene epoxide<br />
Both with vinyl <strong>and</strong> epoxy function<br />
Styrene oxide ( = ethenylphenyloxirane)<br />
Both with vinyl <strong>and</strong> epoxy function 12<br />
Glycidyl methacrylate (GMA) Both with vinyl <strong>and</strong> epoxy function<br />
Epoxidized linseed oil<br />
13<br />
Epoxy methyl soyate<br />
14<br />
Epoxy allyl soyate<br />
14<br />
Vernonia oil<br />
Naturally epoxidized,<br />
E-12,13-epoxyoctadeca-E-9-enoic<br />
acid esters 15–17<br />
Triglycidyl isocyanurate<br />
Triglycidyloxy phenyl silane Flame retardant 18<br />
2-(6-Oxid-6H-dibenz[c,e][1,2]oxaphoshorin-6-yl)-1,4-benzenediol<br />
Flame retardant 19<br />
3,4-Epoxycyclohexyl-methyl- Coatings<br />
3,4-epoxycyclohexane carboxylate<br />
2,3,8,9-Di(tetramethylene)-<br />
Dental applications 20<br />
1,5,7,11-tetraoxaspiro[5.5]undecane<br />
Bis(3,4-epoxy-6-methylcyclohexylmethyl)adipate<br />
Dental applications 20<br />
Epoxidized cyclololefins Multifunctional, c.f. Figure 3.1<br />
Fluoro-epoxides<br />
21<br />
Biphenyl-based epoxies Liquid crystalline, c.f. Figure 3.3<br />
Terephthaloylbis(4-oxybenzoic) acid Liquid crystalline 22<br />
DGEBA adduct<br />
Bis[3-(2,3-epoxypropyl thio)phenyl]- Optical applications 23<br />
sulfone<br />
4,4 ′ -Dihydroxychalcone-epoxy Optical applications 24<br />
oligomer
142 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
<strong>Reactive</strong> Diluent<br />
Table 3.2: <strong>Reactive</strong> Diluents<br />
Phenyl glycidyl ether (PGE)<br />
Styrene oxide<br />
Allyl glycidyl ether<br />
Tetraethyl orthosilicate caprolactone<br />
diol adducts<br />
2-Hydroxy-4(2,3-epoxypropoxy)-<br />
benzophenone<br />
exo-3,6-Epoxy-1,2,3,6-tetrahydrophthalimidocaproic<br />
acid<br />
exo-3,6-Epoxy-1,2,3,6-tetrahydrophthalic<br />
anhydride<br />
Remark/Reference<br />
Cationic curable coatings 25<br />
<strong>Reactive</strong> photostabilizer for wood 26<br />
<strong>Polymers</strong> show anticarcinogenic activity<br />
27<br />
<strong>Polymers</strong> show anticarcinogenic activity28,<br />
29<br />
Table 3.3: Compounds for Glycidyl Functionalization for Epoxide Resins<br />
Compound a<br />
Bisphenol A<br />
Bisphenol F<br />
Phenol novolak<br />
Naphthyl or limonene-modified Bisphenol<br />
A formaldehyde novolak<br />
Cresol novolak<br />
Tetrakis(4-hydroxyphenyl)ethane<br />
p-Aminophenol b<br />
Aminopropoxylate<br />
31<br />
4,4 ′ -Diaminodiphenylmethane b<br />
Hexahydrophthalic acid c<br />
1,3-Bis(3-aminopropyl)tetramethyl-<br />
32<br />
disiloxane<br />
Tetrabromobisphenol A<br />
Bishydantoin<br />
Isocyanurate<br />
Cresol<br />
1,4-Butanediol<br />
Remark/Reference<br />
St<strong>and</strong>ard resins<br />
Improved mechanical properties, reduced<br />
water absorption 30<br />
Increases crosslinking density<br />
Higher reactivity at amine curing<br />
For flame retardant formulations<br />
Powder coatings<br />
<strong>Reactive</strong> diluent<br />
<strong>Reactive</strong> diluent<br />
a : Compounds are epoxidized at the hydroxyl function with epichlorohydrin<br />
b : Compounds epoxidized at the amino function with epichlorohydrin<br />
c : Compounds epoxidized at the carboxyl function with epichlorohydrin
Epoxy Resins 143<br />
HO<br />
CH 2<br />
OH<br />
HO NH 2<br />
Bisphenol-F<br />
p-Aminophenol<br />
HO<br />
OH<br />
CH 3<br />
HO<br />
C<br />
OH<br />
CH 3<br />
CH<br />
CH<br />
Bisphenol-A<br />
HO<br />
OH<br />
H 2 N<br />
CH 2 NH 2<br />
Tetrakis(4-hydroxyphenyl)ethane<br />
4,4’-Diaminodiphenylmethane<br />
OH OH OH<br />
CH 2 CH 2 CH 2<br />
Novolac<br />
Figure 3.2: Compounds for Epoxide Resins
144 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
3.2.3 Specialities<br />
3.2.3.1 Hyperbranched <strong>Polymers</strong><br />
Hyperbranched polymers are highly branched macromolecules that are prepared<br />
through a single-step polymerization process. 33 Many polymers of<br />
this type are also known as dendrimers, because their structure resembles<br />
the branches of a tree. Also, star-like <strong>and</strong> comb-like polymers belong to the<br />
class of hyperbranched polymers. However, hyperbranched polymers are<br />
built up from dendritic, linear, <strong>and</strong> terminal units. They can be synthesized<br />
via three routes:<br />
1. Step-growth polycondensation of AB x monomers,<br />
2. Self-condensing vinyl polymerization of AB∗ monomers,<br />
3. Multibranching ring-opening polymerization of latent AB x monomers.<br />
The methods of synthesis available allow a wide variety of different<br />
polymer types. Further special properties can be imparted by suitable end<br />
capping reactions. This type of polymer has unique properties that are<br />
characteristic for dendritic macromolecules, such as low viscosity, good<br />
solubility, <strong>and</strong> a high functionality.<br />
Dendrimers are used in medical fields, as carriers of organic compounds.<br />
Hyperbranched polymers are easier to synthesize in large quantities<br />
<strong>and</strong> are used as tougheners, plasticizers, antiplasticizers <strong>and</strong> curing<br />
agents.<br />
34, 35<br />
Hyperbranched polymers (HBP) with hydroxyl terminal<br />
groups can initiate curing by a proton donor-acceptor complex. In curing<br />
a tetrafunctional epoxy resin, the activation energy is lower than in an<br />
epoxy system with linear polymers. 36 Hyperbranched polymers strongly<br />
enhance the curing rate due to the catalytic effect of hydroxy groups. 37<br />
The gel time increases with increasing functionality from diglycidyl ether<br />
of bisphenol A (DGEBA) to tetraglycidyl-4,4 ′ -diaminodiphenylmethane<br />
(TGDDM). 38 A hydroxyl-functionalized HBP reduced the gel time of the<br />
blends because of the accelerating effect of -OH groups to the epoxy curing<br />
reaction.<br />
Star-like epoxy polymers can be rooted from polyhydroxy fullerene<br />
with a cycloaliphatic epoxy monomer. 39 Around 8 to 10 epoxy units can<br />
be attached to the fullerene core.<br />
The addition of small amounts of hyperbranched polymer to an epoxy<br />
system enhances dramatically its toughness. The critical strain energy
Epoxy Resins 145<br />
release rate DGEBF resin can be increased by a factor of 6 by the addition<br />
of only 5% of hyperbranched polymer. 40 At higher concentrations, a phase<br />
separation is indicated by two glass transition temperatures. 41<br />
In composite materials, resins modified by hyperbranched polymers<br />
allow higher volume fractions of fibers for producing void-free laminates<br />
in comparison to unmodified resins. 42<br />
3.2.3.2 Liquid Crystalline Epoxide Resins<br />
Initially a few technical terms concerning liquid crystals are recalled. There<br />
are textbooks on liquid crystals, e.g., that of Collings <strong>and</strong> Hird. 43<br />
Liquid Crystal. Liquid crystals were discovered by the Austrian chemist<br />
<strong>and</strong> botanist Friedrich Reinitzer, who found that cholesterol benzoate did<br />
not melt into a clear liquid, but remained turbid. On further heating the<br />
turbid liquid turned suddenly clear. This transition point is now called<br />
the clearing point. For this reason, in addition to the common states of<br />
aggregation, the liquid crystalline state was established. The term liquid<br />
crystal goes back to the German physicist Otto Lehmann.<br />
Liquid crystals are formed mostly by rod-like molecules. They are<br />
sometimes addressed as mesomorphic phases. Materials that can form such<br />
phases are called mesogens. An ordinary fluid is called isotropic, i.e., its<br />
properties are independent of direction. A liquid crystal is orientated, or<br />
likewise an anisotropic liquid. This means that the molecules are oriented<br />
preferably in a certain direction. Such an anisotropic fluid is a nematic liquid<br />
crystal. A liquid crystal more similar to a solid is a smectic phase. Here<br />
the molecules are arranged in layers, but within the layers the molecules<br />
have no fixed positions.<br />
<strong>Polymers</strong>. Liquid crystalline polymers exhibit a number of improved<br />
properties in comparison with traditional plastics, in particular increased<br />
elastic moduli at high temperatures, reduced coefficients of thermal expansion,<br />
increased decomposition onset temperatures, <strong>and</strong> reduced solvent<br />
absorption.<br />
Suitable epoxide monomers are based on biphenyl moieties. 44 Monomers<br />
for liquid crystalline epoxide resins are shown in Figure 3.3. It is<br />
believed that micro-Brownian motion in the polymer chain is increasingly<br />
suppressed as the mesogen concentration increases. This effect causes an
146 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
CH 2 C<br />
H<br />
O<br />
CH 2 O O CH 2 C CH 2<br />
H<br />
O<br />
CH 2 C<br />
H<br />
H 3 C<br />
CH 3<br />
O<br />
CH 2 O O CH 2 C CH 2<br />
H 3 C<br />
CH 3<br />
H<br />
O<br />
CH 2 C<br />
H<br />
O<br />
(CH 2 )n CH 2<br />
O<br />
CH 2<br />
(CH 2 )n<br />
O<br />
C CH 2<br />
H<br />
Figure 3.3: Monomers for Liquid Crystalline Epoxide Resins<br />
increase in the thermal decomposition onset temperatures, a decrease of<br />
the coefficient of thermal expansion, <strong>and</strong> a decrease in water absorption.<br />
When the diglycidyl ether of bisphenol A is cured with sulfanilamide,<br />
a crosslinked network with liquid crystalline properties is obtained. 45<br />
Sulfanilamide has two different amine functions of unequal reactivity. This<br />
causes the formation of a smectic phase when it is used as a curing agent.<br />
Polarized optical microscopy indicates that the epoxy monomer does not<br />
show a liquid cristalline (LC) phase. Also a mixture of sulfanilamide <strong>and</strong><br />
diglycidyl ether of bisphenol A does not show LC properties. An isotropic<br />
liquid is formed above the melting point. However, when the reaction between<br />
epoxy <strong>and</strong> amine proceeds, an LC texture is developed, which is<br />
locked in the crosslinked network by the nematic arrangement.<br />
3.2.4 Manufacture<br />
3.2.4.1 Epoxides<br />
Epoxides can be manufactured by the epoxidation reaction, in particular<br />
1. By direct oxidation,<br />
2. Via peroxyacids,<br />
3. In-situ epoxidation,
Epoxy Resins 147<br />
4. By hypochlorite reaction, <strong>and</strong><br />
5. By reaction with fluoro complexes.<br />
Direct Oxidation. Olefins can epoxidized by oxidizing them in the vapor<br />
phase in the presence of a silver catalyst. The catalyst is activated by<br />
adding small amounts of dichloroethane to the reaction mixture. The direct<br />
oxidation with oxygen is less important for the synthesis of epoxies used<br />
for epoxy resins, in favor of peroxyacids.<br />
Certain Schiff bases that are attached on polymers allow the direct<br />
oxidation of olefins. A polymer bound Schiff base lig<strong>and</strong> is prepared from<br />
poly(styrene) bound salicylaldehyde <strong>and</strong> glutamic acid. With complexes of<br />
these catalysts, cyclohexene, 1-octene, 1-decene, 1-dodecene <strong>and</strong> 1-tetradecene<br />
can be oxidized by molecular oxygen. 46<br />
Peroxyacids. Also, organic peroxides can serve as an oxygen source.<br />
Unsaturated fatty acids <strong>and</strong> their esters are epoxidized with peroxyacetic<br />
acid. Originally peroxybenzoic acid was used, which is highly selective.<br />
However, this reagent is comparatively expensive. Several other peroxyacids<br />
have been investigated; they are in general less efficient. The reaction<br />
of olefins with peroxyacids is a single-step reaction.<br />
Hydrogen peroxide itself is a rather poor epoxidation oxidant, however,<br />
it is used to generate the peroxyacids that are much more active. The<br />
peroxyacids are prepared by reacting hydrogen peroxide with the corresponding<br />
acid. The reaction is an equilibrium reaction. Highly concentrated<br />
peroxyacids can be obtained by adding anhydrides, or removing<br />
the water by azeotropic distillation. Another route to prepare peroxyacids<br />
starts from the anhydride <strong>and</strong> sodium peroxide, in presence of an acid as<br />
catalyst. There should not be even traces of heavy metals present that cause<br />
a loss in activity of the hydrogen peroxide.<br />
For technical synthesis, peroxyacetic acid is used most frequently,<br />
because it has a high equivalent weight, a high efficiency for epoxidation,<br />
<strong>and</strong> a sufficient stability.<br />
In-Situ Epoxidation. The peroxyacids can be regenerated during the<br />
epoxidation reaction with hydrogen peroxide. In this way all the hazards<br />
in preparation <strong>and</strong> h<strong>and</strong>ling of the peroxyacids as such are avoided. The<br />
reaction is heterogeneous <strong>and</strong> the peroxyacid has to be regenerated under<br />
conditions that would result in ring opening of the epoxide. Therefore, only
148 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
fast epoxidation reactions can be conducted utilizing the in-situ technique.<br />
For this reason, the most reactive peroxyacids are also selected. These are<br />
in particular the 3-nitroperoxybenzoic acid <strong>and</strong> 4-nitroperoxybenzoic acid.<br />
Less reactive olefins must still be epoxidized with the peroxyacids<br />
formed in a previous step. The ring opening of the epoxide with the acid<br />
formed from the peroxyacid can be minimized, allowing the phases utmost<br />
separation. This means there should be only small agitation. On the other<br />
h<strong>and</strong>, with certain solvent combinations the epoxide <strong>and</strong> the acid are mutually<br />
insoluble.<br />
Hypochlorite. Partially fluorinated epoxides can be prepared by the oxidation<br />
of the corresponding olefins by NaOCl or NaOBr with phase transfer<br />
catalysts, e.g., methyltricaprylylammonium chloride. 47 For example,<br />
hexafluoroisobutene reacts with the solution of sodium hypochlorite in water<br />
at 0 to 10°C giving the corresponding epoxide in a yield of 65 to 70%.<br />
Fluoro Complex. By reacting diluted fluorine with aqueous acetonitrile,<br />
a complex HOF × CH 3 CN is formed. This complex is a very efficient<br />
oxygen transfer agent. It was shown to be useful to obtain various types<br />
of epoxides that are otherwise difficult to synthesize. The products can be<br />
obtained in a single-step reaction with high yield. 48<br />
3.2.4.2 Glycidyl Ethers<br />
In the simplest case a glycidyl ether for an epoxy resin is prepared by the<br />
reaction of bisphenol A (<strong>and</strong> epichlorohydrin), as pointed out in Figure<br />
3.4. In the first step DGEBA is formed, however, the condensation can<br />
proceed further. The reaction proceeds in two steps. First the epoxide ring<br />
is opened <strong>and</strong> then the ring is formed again, as shown in Figure 3.5.<br />
Hydrogen chloride is evolved during the condensation <strong>and</strong> captured<br />
with caustic soda. The ring opening occurs such that the primary carbon<br />
atom is attacked <strong>and</strong> thus a 1,2-chlorohydrin (ΦCH 2 CH(OH)CH 2 Cl) is<br />
formed, as shown in Figure 3.5.<br />
However in a side reaction the secondary carbon atom is also attacked<br />
<strong>and</strong> thus a 1,3-chlorohydrin (HOCH 2 CH(Φ)CH 2 Cl) is formed. If<br />
the degree of dehydrochloration is not complete, then 1,2-chlorohydrin end<br />
groups also may be present.
Epoxy Resins 149<br />
O<br />
CH 3<br />
CH 2<br />
CH<br />
CH 2 Cl +<br />
HO<br />
C<br />
OH<br />
CH 3<br />
O<br />
CH 3<br />
CH 2<br />
CH<br />
CH 2<br />
O<br />
C<br />
O<br />
O<br />
CH 3<br />
CH 3<br />
CH 2<br />
CH OH<br />
CH 2<br />
n<br />
CH 2<br />
CH<br />
CH 2 O<br />
C<br />
O<br />
CH 3<br />
Figure 3.4: Synthesis of an Epoxide Oligomer<br />
O<br />
OH + CH 2 CH CH 2 Cl<br />
OH<br />
O<br />
CH 2<br />
CH<br />
CH 2<br />
Cl<br />
-HCl<br />
O<br />
O CH 2 CH CH 2<br />
Figure 3.5: Formation of the Glycidyl Ether
150 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Concerning the nomenclature, the situation is confusing. There are<br />
many synonyms for the glycidyl ethers. The Chemical Abstracts name for<br />
diglycidyl ether of bisphenol A (DGEBA) is 2,2 ′ -[(1-Methylethylidene)-<br />
bis(4,1-phenyleneoxymethylene)]bis(oxirane), <strong>and</strong> there are some 12 other<br />
synonyms of chemical names in use, besides the trade names.<br />
We focus back to the main reaction. The newly formed epoxide<br />
groups from the second step of the reaction may again undergo a reaction<br />
with the phenolic group, <strong>and</strong> in the case of a bifunctional phenol, such as<br />
bisphenol A, the molecule grows. The degree of oligomerization (n − 1 in<br />
Figure 3.4) can vary from 1 to approximately 25. The oligomer is liquid at<br />
room temperature when n is smaller than one <strong>and</strong> becomes solid when n is<br />
larger than two.<br />
The degree of polymerization that can be achieved depends on the<br />
ratio of bisphenol A to epichlorohydrin. If epichlorohydrin is in excess,<br />
then the diglycidyl ether will be the main product. Impurities such as water<br />
can substantially decrease the degree of polymerization by side reactions.<br />
Water reacts with epichlorohydrin to form a glycol.<br />
3.2.4.3 Fluorinated Epoxides<br />
The incorporation of fluorine enhances the chemical <strong>and</strong> the thermal stability,<br />
the weathering resistance. Further the surface tension is lowered <strong>and</strong><br />
thus the hydrophobicity is enhanced. Fluorinated epoxy monomers have<br />
been synthesized from fluorinated diols, such as 2,2,3,3,4,4,5,5-octafluoro-hexane-1,6-diol<br />
or 2,2,3,3,4,4,5,5,6,6,7,7,8,8,9,9-hexadecafluoro-decane-1,10-diol<br />
by etherification with allyl chloride <strong>and</strong> subsequent oxidation<br />
of the allyl group. 21 In UV curing, the monomers showed a higher<br />
reactivity than hexanediol diglycidyl ether.<br />
The adduct of 2-chlorobenzotrifluoride <strong>and</strong> glycerol diglycidyl ether<br />
(DGEBTF) has been co-reacted with DGEBA using 4,4 ′ -diaminodiphenylmethane<br />
as hardener. 49 The introduction of the trifluoromethyl group<br />
into the chain of the epoxy resin results in an improvement of the dielectric<br />
<strong>and</strong> mechanical properties. Further the glass transition temperature is<br />
lowered. The glass transition temperature of a pure DGEBA resin is 193°C<br />
whereas the glass transition temperature of the DGEBTF resin is 105 °C.<br />
This indicates that the introduction of fluorine enhances the mobility of the<br />
network.
Compound Class<br />
Table 3.4: Toughening Agents for Epoxy Resins<br />
Epoxy Resins 151<br />
Reference<br />
Poly(ethylene) phthalates<br />
50<br />
Poly(ethylene phthalate-co-ethylene terephthalate)<br />
51<br />
Hyperbranched aliphatic polyester<br />
52, 53<br />
Hyperbranched block copolyethers<br />
54<br />
Epoxidized soyabean oil<br />
14, 55, 56<br />
Copolymers of 2-ethylhexyl acrylate <strong>and</strong> acrylic acid<br />
57<br />
Methacrylic microgels<br />
58<br />
Terpolymers of N-phenylmaleimide, styrene <strong>and</strong> p-hydroxystyrene<br />
59<br />
Triblock copolymer poly(styrene-b-ethylene-co-buteneb-styrene)<br />
60<br />
Poly(benzimidazole)<br />
61<br />
Poly(phenylene oxide<br />
62<br />
Silicon-modified polyurethane oligomers<br />
63<br />
Poly(dimethylsiloxane) polymers<br />
Epoxy-aminopropyltriethoxysilane<br />
64<br />
Poly(ether ether ketones)<br />
65<br />
Polyetherimides<br />
66–68<br />
Carboxylated polymers<br />
69<br />
Phenolic hydroxy-terminated polysulfones<br />
70, 71<br />
Liquid rubbers<br />
72<br />
Liquid rubbers carboxyl-terminated with poly(2-ethylhexyl<br />
73–75<br />
acrylate)<br />
Poly(vinyl acetate)<br />
76<br />
Rubbery epoxy based particles<br />
77<br />
Glass beads<br />
78, 79<br />
3.3 SPECIAL ADDITIVES<br />
3.3.1 Toughening Agents<br />
Highly crosslinked epoxy resins are brittle. For various applications they<br />
need to be toughened. Toughening agents are summarized in Table 3.4. Extensive<br />
literature on toughening of polymers is available. 80–83 The toughening<br />
mechanisms of elastomer-modified epoxy systems are different from<br />
flexibilized epoxy systems.<br />
• Flexibilized epoxy systems reduce mechanical damage through<br />
lowering modulus or plasticization; this allows stress to be relieved
152 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
through distortion of the material. 84<br />
• Elastomer-toughened epoxy systems in general maintain a large<br />
percentage of the modulus <strong>and</strong> temperature resistance of the unmodified<br />
resin system. Stress is absorbed by cavitation of the<br />
elastomer particles <strong>and</strong> shear b<strong>and</strong>ing in the cavitated zone. Elastomer-toughened<br />
epoxy systems can tolerate a certain degree of<br />
damage by preventing growth of a crack. In this way the damaged<br />
region remains local. 85<br />
When using thermoplastic-modified thermosets, compromises between<br />
toughness <strong>and</strong> thermal stability associated with the rubber toughening<br />
of thermosets can be avoided. Another advantage of using the reaction<br />
induced phase separation procedure is that by the adequate selection<br />
of cure cycles <strong>and</strong> initial formulations, a variety of morphologies can be<br />
generated.<br />
However, the fracture toughness is significantly improved with a<br />
nonreactive thermoplastic, only, when bicontinuous or inverted phase structures<br />
are formed. On the other h<strong>and</strong>, when the phase separation produces<br />
thermoplastic-rich particles that are dispersed in a continuous thermosetrich<br />
matrix, little or no improvement of the fracture properties is obtained.<br />
This is mainly due to the poor adhesion between the phases. 60<br />
Basically, functionalized thermoplastics are capable of forming a<br />
chemical linkage between the phases. This interphase bonding could improve<br />
the adhesion properties. However, the reactivity of the modifier can<br />
also complicate the behavior <strong>and</strong> the control of the phase separation process.<br />
3.3.1.1 Polyvinylic Compounds<br />
Many polyvinylic compounds increase the flexibility <strong>and</strong> are used as toughening<br />
agents.<br />
Poly(styrene). Blends of poly(styrene) (PS) with an epoxy monomer<br />
(DGEBA) <strong>and</strong> a tertiary amine, benzyldimethylamine (BDMA), are initially<br />
miscible at 120°C. However, at very low conversions a phase separation<br />
occurs. Here, at the cloud point, a sharp decrease of the light transmittance<br />
is observed. There is a significant difference between the refractive<br />
indices of poly(styrene) <strong>and</strong> the DGEBA/BDMA solution. The refractive<br />
index of the epoxy network increases in the course of polymerization. Due
Epoxy Resins 153<br />
to the continuous increase of the refractive index of the epoxy phase during<br />
curing, finally the refractive indices of both phases match, so that the final<br />
materials at complete conversion appear transparent. 86<br />
Copolymers of Styrene <strong>and</strong> Acrylonitrile. In an epoxy system containing<br />
tetraglycidyl-4,4 ′ -diaminodiphenylmethane (TGDDM) <strong>and</strong> a 4,4 ′ -diaminodiphenylsulfone<br />
(DDS) hardener, blends with poly(styrene-co-acrylonitrile)<br />
(SAN) up to 40 phr show complete miscibility over the entire<br />
range. 87 The glass transition temperature <strong>and</strong> the curing characteristics<br />
can be modelled with various theories. 88 In several systems autocatalytic<br />
curing kinetics is observed. 89–93<br />
Copolymers of Phenylmaleimide, Benzyl methacrylate, <strong>and</strong> Styrene.<br />
The vinylic compounds can be polymerized in-situ during the curing of the<br />
epoxy system. 94 A suitable monomer system consists of three monomers:<br />
phenylmaleimide, benzyl methacrylate, <strong>and</strong> styrene. An advantage is that<br />
by the admixing of the monomers the viscosity of the uncured resins drops<br />
significantly.<br />
Graft <strong>Polymers</strong> of Ethylene/vinyl acetate to Methyl methacrylate. A<br />
graft polymer synthesized by grafting ethylene/vinyl acetate (EVA) onto<br />
poly(methyl methacrylate) thus resulting in a poly(ethylene-co-vinyl acetate)graft-poly(methyl<br />
methacrylate) exhibits a special performance. The<br />
EVA moieties are initially immiscible in the uncured epoxide formulation.<br />
The PMMA moieties are initially miscible, however they separate during<br />
curing. Therefore, EVA-g-PMMA as modifier yields stable dispersions of<br />
EVA blocks, favored by the initial solubility of PMMA blocks. So the<br />
PMMA acts initially as a compatibilizer for the epoxy moieties. 95<br />
Blends of Poly(methyl methacrylate) <strong>and</strong> Poly(ethylene oxide). Blends<br />
of poly(ethylene oxide) (PEO) <strong>and</strong> poly(methyl methacrylate) (PMMA)<br />
form a single phase in the melt. In solid mixtures of these polymers, phase<br />
separation is often observed. In blends of an epoxy resin with PMMA,<br />
PEO acts as a compatibilizer. The morphology of the resulting polymer<br />
mixture may be changed dramatically by only small amounts of PEO. The<br />
stiffness is controlled by the corresponding matrix of the ternary mixture,<br />
but both strength <strong>and</strong> fracture toughness are a function of the resulting<br />
morphology. 96
154 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Poly(benzimidazole). The incorporation of poly(benzimidazole) into a<br />
difunctional epoxy resin matrix enhances both the glass transition temperature<br />
of the matrix <strong>and</strong> its toughness. 61<br />
Multilayer Particles. Multilayer particles of PMMA can be manufactured<br />
formed by emulsion polymerization. They consist of alternate glassy<br />
<strong>and</strong> rubbery layers. The outer layer bears glycidyl groups to allow a chemical<br />
bonding of the particles onto the cured resin. This type of toughening<br />
particles is more effective than acrylic toughening particles or a liquid<br />
carboxyl-terminated butadiene-acrylonitrile rubber. 97<br />
3.3.1.2 Polycondensates<br />
Aromatic polyesters that are prepared from aromatic dicarboxylic acids<br />
<strong>and</strong> 1,2-ethanediol are improving the toughness of bisphenol A diglycidyl<br />
ether epoxy resins. In particular, phthalic anhydride, isophthalic acid, terephthalic<br />
acid <strong>and</strong> 2,6-naphthalene dicarboxylic acid, <strong>and</strong> mixtures of these<br />
compounds are used. The aromatic polyesters are soluble in the epoxy resin<br />
without solvents <strong>and</strong> are effective modifiers for toughening the epoxy<br />
resins. 50 The inclusion of 20% poly(ethylene phthalate) increases the fracture<br />
toughness of a cured resin by 130% with no loss of mechanical <strong>and</strong><br />
thermal properties. 51<br />
Instead of 1,2-ethanediol, 1,4-cyclohexanedimethanol can be used to<br />
obtain poly(1,4-cyclohexylenedimethylene phthalate). 98 Other flexibility<br />
enhancers are polyamide, polyetherimides, 66, 67 carboxylated polymers, 69<br />
phenolic hydroxy-terminated polysulfones, 70 <strong>and</strong> fatty diamines.<br />
Polyetherimide. In blends of an epoxy system of diglycidyl ether of bisphenol<br />
A <strong>and</strong> nadic methyl anhydride, a phase separation occurs by the<br />
addition of polyetherimide in the course of curing. The phase separation is<br />
not observed without polyetherimide. By increasing the amount of polyetherimide<br />
in the blends, the final conversion is decreased. This indicates<br />
that polyetherimide hinders the cure reaction between the epoxy <strong>and</strong> the<br />
curing agent. 99 Homogeneous structures are formed at low polyetherimide<br />
concentration (5 phr). 100<br />
Poly(ether ether ketone). Poly(ether ether ketone) (PEEK) is a tough,<br />
semi-crystalline high performance thermoplastic polymer with good ther-
Epoxy Resins 155<br />
O<br />
O<br />
C<br />
O<br />
C<br />
O<br />
C<br />
O<br />
PEEK-C<br />
H 3 C<br />
CH 3<br />
C<br />
CH3<br />
O<br />
O O C<br />
PEEK-T<br />
Figure 3.6: Poly(ether ether ketone)s<br />
mal <strong>and</strong> mechanical properties. Because of its semi-crystalline nature, it is<br />
difficult to blend this material with epoxy resins.<br />
Phenolphthalein poly(ether ether ketone) (PEEK-C) is miscible with<br />
TGDDM. Several methods, including dynamic mechanical analysis, Fourier-transform<br />
infrared spectroscopy, <strong>and</strong> scanning electron microscopy indicate<br />
that the cured blends are homogeneous. With increasing PEEK-C<br />
content, the tensile properties of the blends decrease slightly. The fracture<br />
toughness factor also decreases. This happens presumably due to the reduced<br />
crosslink density of the epoxy network. Inspection of the fracture<br />
surfaces of fracture toughness test specimens by scanning electron microscopy<br />
shows the brittle nature of the fracture for the pure epoxy resins <strong>and</strong><br />
its blends with PEEK-C. 101 A lower curing temperature favored the homogeneous<br />
morphology in amine cured DGEBA+PEEK-C blends. 102<br />
In general, the processing of blends with PEEK should be easier, by<br />
using PEEK with terminal functional groups <strong>and</strong> bulky pendant groups.<br />
However, poly(ether ether ketone) based on tertiary butyl hydroquinone<br />
(PEEK-T) showed a decreasing rate of reaction with increasing PEEK-T<br />
content. The rate of reaction also decreased with the isothermal curing<br />
temperature. This can be explained by the phase separation. As the curing<br />
reaction proceeds, the thermoplastic component undergoes a phase sepa-
156 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
ration. The separated thermoplastic could retard the curing reaction. The<br />
dispersed particle size increases with the lowering of curing temperature<br />
<strong>and</strong> with an increase in the thermoplastic material added. 65 Poly(ether<br />
ether ketone)s are shown in Figure 3.6.<br />
Chain-extended Ureas. The synthesis of chain-extended ureas runs via<br />
a two-stage process. In the first stage, a prepolymer with isocyanate end<br />
groups is synthesized by the reaction of poly(propylene) glycol <strong>and</strong> toluene<br />
diisocyanate. In the second step, the prepolymer is end-capped with dimethylamine<br />
or imidazole, to result in an amine-terminated chain-extended<br />
urea (ATU) or an imidazole-terminated chain-extended urea, respectively,<br />
with flexible spacers. 103 This type of toughening agent accelerates the curing<br />
of the epoxide groups significantly because of the amino functions in<br />
the molecule.<br />
3.3.1.3 Liquid rubbers<br />
The addition of elastomers to epoxy adhesives can improve peel strength,<br />
fracture resistance, adhesion to oily surfaces <strong>and</strong> ductility. Liquid rubbers,<br />
like carboxyl, amine, or epoxy-terminated butadiene/acrylonitrile rubbers,<br />
are used as toughening agents. 72, 104 Liquid rubber modifiers are initially<br />
miscible with the epoxy resin. However, in the course of curing a phase<br />
separation takes place.<br />
Carboxy-terminated butadiene/acrylonitrile copolymers (CTBN) are<br />
particularly suitable because of their miscibility in many epoxy resins. The<br />
carboxyl group can react easily with an epoxy group. If a CTBN is not<br />
prereacted with an epoxy resin, the carboxylic acid groups can react during<br />
curing.<br />
Solid acrylonitrile-butadiene rubbers (NBR), in particular with high<br />
content of acrylonitrile are also suitable tougheners. 105 A high content of<br />
acrylonitrile in the rubber imparts better compatibility between NBR <strong>and</strong><br />
the epoxy resin.<br />
3.3.1.4 Silicone Elastomers<br />
CTBN <strong>and</strong> amine-terminated butadiene-acrylonitrile elastomers (ATBN)<br />
lose the desired mechanical properties in the high temperature region <strong>and</strong><br />
in the low temperature region. Silicone rubbers are superior in this aspect.<br />
However, silicone rubbers are completely immiscible with epoxy resins
Epoxy Resins 157<br />
<strong>and</strong> cannot be used for this reason. The addition of a silicone grafted poly-<br />
(methyl methacrylate) is effective to stabilize the interface of the silicone<br />
rubber <strong>and</strong> the epoxy resin <strong>and</strong> helps to disperse the silicone rubber in the<br />
epoxide matrix in this way. The molecular weight of the silicone segment<br />
strongly affects the effectiveness of the compatibilizer. With increasing<br />
particle diameter of the silicone the fracture toughness decreases <strong>and</strong> drops<br />
eventually below the unmodified resin. 106<br />
For a carboxyl-terminated dimethyl siloxane oligomer used as a rubber<br />
modifier, aramid/silicone block copolymers were used as compatibilizers.<br />
107 The aramid-type blocks have phenolic groups on the aromatic rings.<br />
These groups can react with the epoxy resin to cause the compatibilization.<br />
3.3.1.5 Rubbery Epoxy Compounds<br />
Instead of liquid rubber, rubbery epoxy based particles obtained from an<br />
aliphatic epoxy resin can be blended with another epoxy resin to act as<br />
toughening agents themselves. 77 One of the limitations of epoxy-CTBN<br />
adducts is their high viscosity; however, there are also low-viscosity types<br />
available.<br />
3.3.1.6 Phase Separation<br />
During curing of polymer resin blends, a phase separation occurs. The<br />
phase separation can be characterized by<br />
1. Small angle X-ray scattering,<br />
2. Light transmission,<br />
3. Light scattering,<br />
4. Transmission electron microscopy, <strong>and</strong><br />
5. Atomic force microscopy.<br />
The viscosity at the cloud point can have a strong effect on the final<br />
morphology <strong>and</strong> mechanical properties of the resin. The phase separation<br />
mechanisms are dependent on the initial modifier concentration <strong>and</strong> on the<br />
ratio of the phase separation rate to the curing rate. The curing temperature<br />
has a strong effect on the extent of phase separation. Annealing allows the<br />
phase separation process to proceed further. 67<br />
The extent of phase separation depends on the cure cycle, as shown<br />
in blends of a st<strong>and</strong>ard epoxy resin <strong>and</strong> poly(methyl methacrylate). The
158 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
extent of phase separation can be diminished or suppressed by longer precuring<br />
times at lower temperatures, before the main curing is started. 108<br />
In addition, the phase separation can be controlled by the choice of<br />
the curing agents. In the case of poly(methyl methacrylate) as modifier, in<br />
an epoxy system, based on DGEBA some hardeners effect a phase separation<br />
before gelation <strong>and</strong> others do not. For example, 4,4 ′ -diaminodiphenylsulfone<br />
(DDS) <strong>and</strong> 4,4 ′ -methylenedianiline (MDA) result in a phase separation,<br />
but for 4,4 ′ -methylene bis(3-chloro-2,6-diethylaniline) (MCDEA)<br />
no phase separation is observed. 109<br />
3.3.1.7 Preformed Particles<br />
Preformed particles do not require phase separation <strong>and</strong> remain in that<br />
shape in which they were added to the neat resin or composite. Therefore,<br />
these particles may be synthesized prior to the resin formulation <strong>and</strong><br />
then added to the thermosetting resin or formed in-situ, i.e., during the<br />
formulation of the resin, before the resin is cured. 110<br />
Prereacted urethane microspheres can be formed by dynamic vulcanization<br />
method in liquid diglycidyl ether of bisphenol A. The prereacted<br />
particles are then added to an uncured epoxy resin system <strong>and</strong> cured. The<br />
mechanical <strong>and</strong> adhesion properties do not depend on any curing condition<br />
of epoxy resin because the particles are stable, in contrast to a process<br />
where a phase separation occurs during curing. 111<br />
3.3.1.8 Inorganic Particles<br />
In contrary to rubber, the toughening of inorganic particles is rather modest.<br />
However, the toughening by inorganic particles has an advantage insofar<br />
as it can also improve the modulus. Rubber toughens such that the<br />
increase in toughness is accompanied at the expense of a decrease in the<br />
modulus.<br />
The toughening of inorganic particles is explained by the crack front<br />
bowing mechanism. 112–114 A crack front increases its length by changing<br />
its shape when it interacts with two or more inhomogeneities in a brittle<br />
material. The inorganic particles inside the polymer matrix can resist a<br />
crack propagation.<br />
When a crack propagates in a rigid particle filled composite, the rigid<br />
particles try to resist. Because of this resistance, the primary crack front has<br />
to change its direction between the rigid particles (bowing), thus forming
Epoxy Resins 159<br />
a secondary crack front. The bowed secondary crack front now has more<br />
elastic energy stored than the straight unbowed crack front. A crack front<br />
starts to bow out between particles, when it meets the particles.<br />
Microcracking with debonding has been proposed as one of the<br />
toughening mechanisms of glass bead-filled epoxies. Three types of micro-mechanical<br />
deformations can be distinguished: 78<br />
1. Step formation<br />
2. Debonding of glass beads <strong>and</strong> diffuse matrix shear yielding<br />
3. Micro-shear b<strong>and</strong>ing<br />
Among the micro-mechanical deformations, micro-shear b<strong>and</strong>ing is<br />
considered the major toughening mechanism for glass bead-filled epoxies.<br />
Step formation <strong>and</strong> combined debonding <strong>and</strong> diffuse matrix yielding are<br />
secondary toughening mechanisms. 79<br />
3.3.2 Antiplasticizers<br />
Antiplasticizers are additives for increasing the strength <strong>and</strong> modulus of<br />
the respective material. They act via strong interactions with the epoxide<br />
matrix. Epoxides with antiplasticizers characteristically 115<br />
1. Have a sufficiently high value of the glass transition temperature<br />
as needed for the applications,<br />
2. Exhibit a higher modulus <strong>and</strong> higher toughness around room temperature,<br />
3. Exhibit a lower water uptake at equilibrium.<br />
Antiplasticizers for epoxide resins are shown in Table 3.7. The addition<br />
of the reaction product of 4-hydroxyacetanilide <strong>and</strong> 1,2-epoxy-3-phenoxypropane<br />
(EPPHAA) to an epoxide resin increases the tensile strength<br />
<strong>and</strong> the shear modulus of the cured system. 116 The mechanism of antiplasticization<br />
can be formulated in terms of hindrance of the short-scale cooperative<br />
motions in the glassy state as a dynamic coupling between the<br />
epoxy polymer <strong>and</strong> the antiplasticizer molecule. 117<br />
In systems where the antiplasticizers have a poor affinity to the resin,<br />
a phase separation during curing occurs. The mobility of the constituting<br />
groups can be characterized by nuclear magnetic resonance techniques. 118
160 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
OH<br />
O<br />
O CH 2 CH CH 2 O NH C<br />
CH 3<br />
EPPHAA<br />
OH<br />
O CH 2 CH CH 2 O CH 3<br />
AM<br />
CH 3<br />
AO<br />
O<br />
O CH 2 CH CH 2 O<br />
CH 3<br />
Figure 3.7: Antiplasticizers for Epoxide Resins<br />
3.3.3 Lubricants<br />
In automotive, aviation <strong>and</strong> the related industries, there is a tendency to use<br />
metallic materials with polymeric materials. For many parts in such applications,<br />
good tribological properties are required. 119 Fluorinated polymers<br />
are known as low friction materials. This property arises due to their low<br />
surface energies.<br />
Fluorinated poly(aryl ether ketone) (12F-PEK) can be added to epoxy<br />
resins to improve the tribological properties. At low concentrations<br />
of 12F-PEK, homogeneous systems are obtained after curing. Above 10%<br />
12F-PEK, a phase separation is observed. At still higher concentrations,<br />
an inversion of the morphology is observed. With fluoropolymer concentrations<br />
of 10% 12F-PEK, a friction reduction of 30% can be obtained. 120<br />
3.3.4 Adhesion Improvers<br />
Epoxy polyurethane hybrid resins are used in high strength adhesives. Elastomer-modified<br />
resins are used for adhesive formulations that cure under<br />
water.
Material<br />
Table 3.5: Reinforcing Materials for Epoxides<br />
Remark/Reference<br />
Epoxy Resins 161<br />
Glass fibers<br />
121–123<br />
Hollow glass fibers<br />
124<br />
Carbon fibers<br />
125–127<br />
Carbon nanotubes<br />
128–131<br />
Graphite<br />
132–138<br />
Aluminum<br />
139, 140<br />
Boron<br />
Aluminum borate whiskers<br />
141<br />
Paper<br />
Poly(ethylene) fibers<br />
Polyaramid Fabric Low density <strong>and</strong> extremely high strength<br />
Cotton<br />
Flax<br />
142<br />
3.3.5 Conductivity Modifiers<br />
To modify the thermal <strong>and</strong> electrical properties, thermally <strong>and</strong> electrically<br />
conductive materials are added.<br />
3.3.6 Reinforcing Materials<br />
3.3.6.1 Composites <strong>and</strong> Laminates<br />
Composites <strong>and</strong> laminates are made by reinforcing the polymers with continuous<br />
fibers. About 1/4 of the epoxy resins are reinforced materials. Reinforcing<br />
materials are shown in Table 3.5. Traditional composite structures<br />
are usually made of glass, carbon, or aramid fibers. The advances<br />
in the development of natural fibers in genetic engineering <strong>and</strong> in composite<br />
science offer significant opportunities for improved materials from<br />
renewable resources with enhanced support for sustainable applications.<br />
Biodegradable composites from biofibers <strong>and</strong> biodegradable polymers will<br />
serve to solve environmental problems. 143<br />
Often the surface of the fiber is chemically modified to increase the<br />
adhesion properties to the resin matrix. For example, glass fibers are coated<br />
with a silane coupling agent. The interfacial bonding between carbon fiber<br />
<strong>and</strong> epoxy resin can be improved by modification with poly(pyrrole). Poly-<br />
(pyrrole) (PPy) can be deposited on carbon fibers via the oxidation-polymerization<br />
of pyrrole (Py) with ferric ions. 144
162 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Laminates are used for insulations. Impregnated sheets of woven<br />
glass, paper, <strong>and</strong> polyaramid fabric or cotton are laminated in large presses.<br />
These sheets are used for printed circuit boards in the electronics industry.<br />
3.3.6.2 Nanocomposites<br />
Polymer nanocomposites, in particular polymer-layered silicate nanocomposites,<br />
are a radical alternative to macroscopically filled polymers. The<br />
preparation of epoxy resin-based nanocomposites was first described by<br />
Messersmith <strong>and</strong> Giannelis. 145 Extensive work on epoxy based nanocomposites<br />
has been done <strong>and</strong> is reviewed among other polymers in the literature.<br />
146, 147<br />
Organoclays. Organoclays are used as precursors for nanocomposites in<br />
many polymer systems. Usually montmorillonite is used for organoclays.<br />
Montmorillonite belongs to the 2:1 layered silicates. Its crystal structure<br />
consists of layers of two silica <strong>and</strong> a layer of either aluminum hydroxide<br />
or magnesium hydroxide. Water <strong>and</strong> other polar molecules can enter between<br />
the unit layers because of the comparatively weak forces between<br />
the layers. Substitution of the ions originally in the layers by such ions<br />
with different charges generates charged interlayers. The stacked array of<br />
clay sheets separated by a regular spacing is addressed as gallery.<br />
For true nanocomposites, the clay nanolayers must be uniformly dispersed<br />
in the polymer matrix, to avoid larger aggregations. Small aggregations<br />
are still addressed as nanocomposites, as intercalated nanocomposites,<br />
ordered exfoliated nanocomposites, <strong>and</strong> disordered exfoliated nanocomposites.<br />
148 Originally, intercalation was the insertion of an extra day<br />
into a calendar year. Exfoliation refers to the peeling of rocky materials<br />
into sheets due to weathering.<br />
Clay nanolayers in elastomeric epoxy matrices dramatically improve<br />
both the toughness <strong>and</strong> the tensile properties. 145, 149 The dimensional stability,<br />
the thermal stability <strong>and</strong> the chemical resistance can also be improved<br />
with clay nanolayers. 150<br />
Exfoliated clays are formed when the clay layers are well separated<br />
from one another <strong>and</strong> individually dispersed in the continuous polymer matrix.<br />
Since exfoliated nanocomposites exhibit a higher phase homogeneity<br />
than the intercalated clays, exfoliated clays are more effective in improving<br />
the properties of the nanocomposites.
Epoxy Resins 163<br />
Successful nanocomposite synthesis depends not only on the cure<br />
kinetics of the epoxy system but also on the rate of diffusion of the curing<br />
agent into the galleries, because it affects the intragallery cure kinetics.<br />
The nature of the curing agent influences these two phenomena substantially<br />
<strong>and</strong> therefore the resulting structure of the nanocomposite. The curing<br />
temperature controls the balance between the extragallery reaction rate<br />
of the epoxy system <strong>and</strong> the diffusion rate of the curing agent into the galleries.<br />
151 It was found that the activity energy decreases with the addition<br />
of organic montmorillonite. 152 Hexahydrophthalic anhydride (HHPA) is<br />
usually used for hot curing of epoxy resins. With an alkoxysilane, it also<br />
acts as a condensation agent. 153 Hot curing of montmorillonite-layered<br />
silicates has been described with methyltetrahydrophthalic anhydride. 154<br />
An exfoliated epoxy-clay nanocomposite structure can be synthesized<br />
by loading the clay gallery with hydrophobic onium ions <strong>and</strong> then<br />
allowing diffusion in the epoxide <strong>and</strong> a curing agent. The degree of exfoliation<br />
increases with decreasing curing agent. 155 Clays exert catalytic<br />
effects on the curing of epoxy resins. 156<br />
An organically modified montmorillonite, prepared by a cation exchange<br />
reaction between the sodium cation in montmorillonite <strong>and</strong> dimethyl<br />
benzyl hydrogenated tallow ammonium chloride is suitable for high<br />
degrees of filling for epoxy resins. 157 Nanocomposites exhibit a significant<br />
increase in thermal stability in comparison to the original epoxy resin. 158<br />
Quaternary ammonium ions both catalyze the epoxy curing reactions<br />
<strong>and</strong> plasticize the epoxy material. This causes a large reduction in<br />
glass transition temperature <strong>and</strong> lowers the storage modulus. Plasticization<br />
is small for aromatic epoxy resins, but large for aliphatic resins. Therefore,<br />
aromatic epoxy-clay systems may result in a complete exfoliation<br />
of the clay galleries, whereas mixtures of aliphatic <strong>and</strong> aromatic epoxy<br />
may produce intercalated systems. 159 Poly(oxypropylene)amine intercalated<br />
montmorillonite is highly organophilic <strong>and</strong> compatible with epoxy<br />
materials. 160<br />
Star branched functionalized poly(propylene oxide-block-ethylene<br />
oxide) was used with an organophilic modified synthetic fluorohectorite as<br />
compatibilizer for nanocomposites. The polarity of the polyol could be tailored<br />
by the type of functionalization. A mixture of two epoxy resins, tetraglycidyl<br />
4,4 ′ -diaminodiphenylmethane <strong>and</strong> bisphenol A diglycidyl ether,<br />
cured with 4,4 ′ -diaminodiphenylsulfone, was used as matrix material. 161<br />
The hybrid nanocomposites were composed of intercalated clay particles
164 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 3.6: Interpenetrating Polymer Networks<br />
Epoxide Further Component Reference<br />
Diglycidyl ether of<br />
bisphenol A<br />
Aliphatic epoxide resin<br />
Unsaturated polyesters<br />
162<br />
Vinylester resin (Bisphenol A<br />
glycidylmethacrylate adduct in<br />
styrene with layered<br />
silicate nanoparticles)<br />
Bisphenol A diacrylate<br />
163<br />
Diglycidyl ether of<br />
bisphenol A<br />
Epoxide bismaleimide resin Cyanate ester<br />
164<br />
Epoxide-amine network Silica<br />
165<br />
Diglycidyl ether of Hexakis(methoxymethyl)melamine<br />
166<br />
bisphenol A<br />
Novolak epoxy resin 2,2 ′ -Diallyl bisphenol A (DBA)<br />
167<br />
Epoxy resin Polyaniline<br />
168<br />
10<br />
as well as separated PPO spheres in the epoxy matrix. Phenolic alkylimidazolineamides<br />
were also used to exchange the interlayer sodium cations of<br />
the layered silicates. 169<br />
Electric capacitors based on epoxy clay nanocomposites can be integrated<br />
into electronic devices. 170<br />
3.3.7 Interpenetrating Polymer Networks<br />
Interpenetrating polymer networks are ideally compositions of two or more<br />
chemically distinct polymer networks held together exclusively by their<br />
permanent mutual entanglements. 171 In practice, interactions of both networks<br />
beyond entanglement may occur, for instance, intercrosslinking.<br />
In a simultaneous interpenetrating polymer network, the two network<br />
components are polymerized concomitantly. In a sequential interpenetrating<br />
polymer network, the first network is formed <strong>and</strong> then swollen<br />
with a second crosslinking system, which is subsequently polymerized.<br />
Interpenetrating polymer networks are known to remarkably suppress<br />
creep phenomena in polymers. The motion of the segments in interpenetrating<br />
polymer networks is diminished by the entanglement between<br />
the networks.<br />
Interpenetrating polymer networks including epoxide resins as one<br />
of the components are summarized in Table 3.6.
Epoxy Resins 165<br />
3.3.7.1 Curing Kinetics<br />
If a thermosetting system is cured at a temperature below its maximally attainable<br />
glass transition temperature, vitrification occurs during cure. The<br />
vitrification slows down the reaction. The reaction may freeze before<br />
reaching full conversion.<br />
In contrast, in an interpenetrating network, if one component (I) reacts<br />
more slowly than the other component (II), the former component (I)<br />
may act as a plasticizer of the polymeric component (II). This allows a<br />
faster reaction of the second component (II) <strong>and</strong> a more thorough cure<br />
without vitrification. 172<br />
In the simultaneous curing of a vinylester resin (VER) <strong>and</strong> an epoxy<br />
resin a reduction in reaction rate due to the dilution of each reacting system<br />
by the other resin components is observed.<br />
The radical polymerization of an acrylate monomer is hardly affected<br />
by the oxygen inhibition effect, while the cationic polymerization<br />
of an epoxy monomer is enhanced by the atmosphere humidity. 173<br />
The decomposition of peroxides is known to be accelerated by amines.<br />
In fact, if for the radical curing of the vinylester component peroxides<br />
are used instead of azo compounds, a strong redox interaction between the<br />
peroxide <strong>and</strong> the amine used for curing the epoxide component is observed.<br />
In such systems the peroxide decomposes too quickly to develop its full<br />
power for curing the vinylester system.<br />
Further, there is an interaction between the vinyl groups of the vinylester<br />
system <strong>and</strong> the amine via a Michael addition. The curing performance<br />
of the epoxide resin is less affected by the radical initiator. 174<br />
3.3.7.2 Unsaturated Polyesters<br />
In mixtures of epoxy based on diglycidyl ether of bisphenol A <strong>and</strong> unsaturated<br />
polyesters, the curing monitored with differential scanning calorimetry<br />
indicated a higher rate constant than the pure epoxide resin. It<br />
is believed that the hydroxyl end group of the unsaturated polyester in the<br />
blend provides a favorable catalytic environment for the epoxide curing. 162<br />
The interpretation of the viscosity development suggests that an interlock<br />
between the two growing networks exists that causes a retarded<br />
increase of the viscosity. 175 The introduction of unsaturated polyester into<br />
epoxy resin improves toughness but reduces the glass transition temperature.<br />
176
166 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Functional Peroxides. Peroxy ester oligomers can be obtained by condensation<br />
of anhydrides with poly(ethylene glycol)s <strong>and</strong> tert-butyl hydroperoxide.<br />
Suitable anhydrides are pyromellitic dianhydride <strong>and</strong> the tetrachloroanhydride<br />
of pyromellitic anhydride. The resulting esters contain<br />
carboxylic groups <strong>and</strong> peroxy groups. These compounds can be used as<br />
curing agents for unsaturated polyesters as such <strong>and</strong> for hybrid resins consisting<br />
of an epoxy resin <strong>and</strong> an unsaturated polyester resin. 177<br />
3.3.7.3 Acrylics<br />
For interpenetrating polymer networks consisting of diglycidyl ether of<br />
bisphenol A (DGEBA) <strong>and</strong> bisphenol A diacrylate as radically polymerizable<br />
component, 4,4 ′ -methylenedianiline <strong>and</strong> dibenzoyl peroxide are suitable<br />
curing agents. The curing can be achieved between 65°C <strong>and</strong> 80°C.<br />
The kinetics of curing of the epoxide takes place as a combination of an uncatalyzed<br />
bimolecular reaction <strong>and</strong> a catalyzed termolecular reaction. The<br />
kinetics of curing of the acrylate runs according to a first-order reaction. 163<br />
In the mixture, the rate constants are lower than in the separate systems.<br />
Also the activation energies in the mixtures are higher. It is believed<br />
that chain entanglements between the two networks cause a steric<br />
hindrance for the curing process. The vitrification restrains the chain mobility<br />
that is reflected as a decrease of the rate constants. The incorporation<br />
of the methacryloyl moiety in an epoxide resin improves the weathering<br />
stability <strong>and</strong> the photostability of the system.<br />
178, 179<br />
3.3.7.4 Urethane-modified Bismaleimide<br />
Urethane-modified bismaleimide (UBMI) can be introduced <strong>and</strong> partially<br />
grafted to the epoxy oligomers by polyurethane grafting agents. Afterwards,<br />
a simultaneous bulk polymerization technique can be used to prepare<br />
interpenetrating networks. 180 The tensile strength increases to a maximum<br />
value with increasing UBMI content, then decreases with further increasing<br />
UBMI content. If the polyurethane grafting agent contains poly-<br />
(oxypropylene) polyols the interpenetrating network shows a two-phase<br />
system, whereas in the case of poly(butylene adipate) a single phase system<br />
is observed. The better compatibility of poly(butylene adipate) base<br />
networks results in a higher impact strength.<br />
An intercrosslinked network of bismaleimide-modified polyurethane-epoxy<br />
systems was prepared from the bismaleimide having ester link-
Epoxy Resins 167<br />
ages, polyurethane-modified epoxy, <strong>and</strong> cured in the presence of 4,4 ′ -diaminodiphenylmethane.<br />
Infrared spectral analysis was used to confirm the<br />
grafting of polyurethane into the epoxy skeleton. The prepared matrices<br />
were characterized by mechanical, thermal, <strong>and</strong> morphological studies.<br />
The changes of the properties depend on the relative amounts of the<br />
moieties used. The incorporation of polyurethane into the epoxy skeleton<br />
increases the mechanical strength <strong>and</strong> decreases the glass transition temperature,<br />
thermal stability, <strong>and</strong> heat distortion temperature. On the other<br />
h<strong>and</strong>, the incorporation of bismaleimide with ester linkages into a polyurethane-modified<br />
epoxy system increases the thermal stability, tensile <strong>and</strong><br />
flexural properties, <strong>and</strong> decreases the impact strength, glass transition temperature,<br />
<strong>and</strong> heat distortion temperature. 181<br />
3.3.7.5 Electrically Conductive Networks<br />
Electrically conductive polymers could find use in rechargeable batteries,<br />
conducting paints, conducting glues, electromagnetic shielding, antistatic<br />
formulations, sensors, electronic devices, light-emitting diodes, coatings,<br />
<strong>and</strong> others. Low concentrations of polyaniline can make the polymer<br />
electrically conductive when a co-continuous microstructure could be<br />
achieved.<br />
For the preparation of conductive polyaniline epoxy resin composites,<br />
a doped polyaniline is blended with the epoxy resin. Plasticizers are<br />
added to assist in the dispersion of the conductive polymer. The curing<br />
agent must be selected in order to avoid dedoping. 168<br />
The grafting onto the nitrogen of polyaniline was achieved by the<br />
ring-opening graft copolymerization of 1,2-epoxy-3-phenoxypropane. By<br />
the degree of grafting, the solubility, the optical <strong>and</strong> the electrochemical<br />
properties of the grafted polyaniline can be tailored. 182<br />
3.3.8 Organic <strong>and</strong> Inorganic Hybrids<br />
An organic-inorganic hybrid interpenetrating network has been synthesized<br />
from an epoxide-amine system <strong>and</strong> tetraethoxysilane (TEOS). The<br />
kinetics of the formation of the silica structure in the organic matrix, <strong>and</strong> its<br />
final structure <strong>and</strong> morphology, depend on the method of preparation of the<br />
interpenetrating network. In the sol gel process, hydrolysis <strong>and</strong> polymerization<br />
of TEOS are performed at room temperature in isopropyl alcohol.<br />
The hybrid network can be prepared by two procedures.
168 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
In the one-step procedure, all reaction components are mixed simultaneously.<br />
In the two-step procedure, TEOS is hydrolyzed in the first step,<br />
then mixed with the organic epoxy components <strong>and</strong> polymerized under the<br />
formation of silica <strong>and</strong> epoxide networks.<br />
Large compact silica aggregates, with 100 to 300 nm diameter, are<br />
formed by the one-stage process of polymerization. In the two-stage process<br />
the partial hydrolysis of TEOS effects an acceleration of the gelation.<br />
This results in somewhat smaller silica structures. The most homogeneous<br />
hybrid morphology with the smallest silica domains of size 10 to 20<br />
nm can be achieved in a sequential preparation of the interpenetrating network.<br />
165, 183<br />
An increase in modulus by two orders of magnitude was<br />
achieved at a silica content below 10%. 184 Phenolic novolak/silica <strong>and</strong><br />
cresol novolak epoxy/silica hybrids can be prepared in a similar manner<br />
with TEOS. 185<br />
3.3.9 Flame Retardants<br />
Flame retardancy can be imparted by suitable monomers <strong>and</strong> curing agents.<br />
Flame retardants can be grouped into halogen-containing compounds, the<br />
most important being tetrabromobisphenol A, halogen free systems containing<br />
aluminum trihydrate with red phosphorus, <strong>and</strong> phosphate esters. 186<br />
Flame retardants that are used in epoxide resins are shown in Table 3.7.<br />
Triglycidyloxy phenyl silane cured with 4,4 ′ -diaminodiphenylmethane<br />
<strong>and</strong> others gives highly flame retardant polymers. 18 Heating in air<br />
indicates that a silicon-containing carbon residue formed is superior in preventing<br />
oxidative burning.<br />
9,10-Dihydro-9-oxa-10-phosphaphenanthrene-10-oxide (DOPO) is<br />
synthesized by a multi step reaction from o-phenylphenol <strong>and</strong> phosphorus<br />
trichloride.<br />
From this compound, an adduct with p-benzoquinone, 2-(6-oxid-<br />
6H-dibenz[c,e][1,2]oxa-phosphorin-6-yl)-1,4-benzenediol (ODOPB), can<br />
be obtained. ODOPB can be used as a reactive flame-retardant in o-cresol<br />
formaldehyde novolak epoxy resins for electronic applications. 19, 187 A related<br />
compound, 2-(6-Oxid-6H-dibenz[c,e][1,2]oxaphosphorin-6-yl)methanol<br />
(ODOPM) can be used as flame-retardant hardener for o-cresol-formaldehyde<br />
novolak epoxy (CNE) resin in electronic applications. 188 Some<br />
phosphorous-containing flame retardants are shown in Figure 3.9.
Epoxy Resins 169<br />
Compound<br />
Table 3.7: Flame Retardants for Epoxide Resins<br />
Remark/Reference<br />
Tetrabromobisphenol A-based epoxies<br />
Triglycidyloxy phenyl silane<br />
18<br />
9,10-Dihydro-9-oxa-10-phosphaphenanthrene-10-oxide<br />
(DOPO)<br />
10-(2,5-Dihydroxyphenyl)-9,10-dihydro-9-oxa-<br />
190<br />
10-phosphaphenanthrene-10-oxide (DHPDOPO)<br />
19, 189<br />
Bis(m-aminophenyl)methylphosphine oxide (BAMPO)<br />
Bismaleimide(3,3 ′ -bis(maleimidophenyl))<br />
192<br />
phenylphosphine oxide (BMPPPO)<br />
Bis(3-glycidyloxy)phenylphosphine oxide<br />
193<br />
Bis(4-aminophenoxy)phenylphosphine oxide (BAPP)<br />
194<br />
Tris(2-hydroxyphenyl)phosphine oxides<br />
195, 196<br />
Bis(3-diethylphosphono-4-hydroxyphenyl)sulfide (DPHS)<br />
197<br />
Benzoguanamine-modified phenol biphenylene components<br />
198<br />
Melamine phosphate<br />
199<br />
2,4,6-Tris(2,4,6-tribromophenoxy)-1,3,5-triazine<br />
200 a<br />
2,2 ′ -[(1-Methylethylidene)bis[(2,6-dibromo-4,1-phenylene)<br />
200 a<br />
oxy]]bis[4,6-bis[(2,4,6-tribromophenyl)oxy]]-1,3,5-triazine<br />
Carbon black<br />
201<br />
a c.f. Figure 3.8<br />
191
170 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Br<br />
Br<br />
Br<br />
Br<br />
O<br />
N<br />
O<br />
Br<br />
N<br />
N<br />
Br<br />
O<br />
Br<br />
Br<br />
Br<br />
Br<br />
Br<br />
Br<br />
Br<br />
O<br />
N<br />
O<br />
Br<br />
N<br />
N<br />
Br<br />
O<br />
Br<br />
Br<br />
H 3 C<br />
C<br />
CH 3<br />
Br<br />
O<br />
Br<br />
Br<br />
N<br />
N<br />
Br<br />
O<br />
N<br />
O<br />
Br<br />
Br<br />
Br<br />
Br<br />
Figure 3.8: Top: 2,4,6-Tris(2,4,6-tribromophenoxy)-1,3,5-triazine,<br />
Bottom: 2,2 ′ -[(1-Methylethylidene)bis[(2,6-dibromo-4,1-phenylene)oxy]]<br />
bis[4,6-bis[(2,4,6-tribromophenyl)oxy]-1,3,5-triazine 200
Epoxy Resins 171<br />
O<br />
P O<br />
CH 2<br />
OH<br />
O<br />
HO<br />
P<br />
O<br />
OH<br />
ODOPM<br />
ODOPB<br />
Figure 3.9: 2-(6-Oxid-6H-dibenz[c,e][1,2]oxaphosphorin-6-yl)methanol<br />
(ODOPM), 2-(6-Oxid-6H-dibenz[c,e][1,2]oxa-phosphorin-6-yl)-1,4-benzenediol<br />
(ODOPB)<br />
Other phosphorus-containing epoxy resins can be obtained from the<br />
addition reaction of DOPO <strong>and</strong> the glycidyl ether of cresol-formaldehyde<br />
novolak. 202, 203 The cured products are highly flame resistant.<br />
In the presence of a phosphorous-containing hardener, bis(m-aminophenyl)methylphosphine<br />
oxide (BAMPO), the volatilization of the cured<br />
resin is reduced <strong>and</strong> aromatization is accelerated. This results in a larger<br />
yield of stable char. This behavior is attributed to the flame retardant action<br />
of BAMPO. However, at high content of BAMPO this effect is overwhelmed<br />
by flame quenching due to the volatilization of the phosphoruscontaining<br />
moieties from BAMPO. 191<br />
Further, bismaleimide(3,3 ′ -bis(maleimidophenyl))phenylphosphine<br />
oxide (BMPPPO), is a phosphorus-containing compound that is soluble in<br />
organic compounds. Interpenetrating networks can be prepared by simultaneously<br />
curing an epoxy/diaminodiphenylmethane system <strong>and</strong> BMPPPO.<br />
The cured resin system exhibits a glass transition temperature around<br />
212°C, thermal stability at temperatures beyond 350°C, <strong>and</strong> excellent flame<br />
retardancy with a limiting oxygen index (LOI) of 40%. 192<br />
Phosphorous-containing diamines have been prepared that act as<br />
curing agents for epoxy resins. 204 The compounds <strong>and</strong> their synthesis<br />
are shown in Figure 3.10. When cured with phosphorus-containing curing<br />
agents, the epoxy resins show extremely high LOI values of up to 49.<br />
Amine-based curing agents destabilize a brominated epoxy resin by<br />
a mechanism of the nucleophilic substitution of bromine. As a result, a<br />
brominated epoxy resin releases products of pyrolysis about 100°C lower<br />
than a nonbrominated epoxy resin. 205
172 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
H 2 N<br />
O<br />
C NH 2<br />
O<br />
P<br />
+<br />
H<br />
O<br />
P<br />
O<br />
H 2 SO 4 /HNO 3<br />
O 2 N<br />
O<br />
P<br />
NO 2<br />
SnCl 2 /HCl/EtOH<br />
H 2 N<br />
O<br />
P O<br />
C NH 2<br />
H 2 N<br />
O<br />
P<br />
NH 2<br />
O<br />
P<br />
O<br />
2-DOPO-A<br />
BAPPPO<br />
Figure 3.10: 2-DOPO-A, Bis(4-aminophenyl)phenylphosphine oxide<br />
(BAPPO)<br />
204, 206
Epoxy Resins 173<br />
Table 3.8: Global Production/Consumption Data of Important Monomers<br />
<strong>and</strong> <strong>Polymers</strong> 207<br />
Monomer Mill. Metric tons Year Reference<br />
Ethylene oxide 14.7 2002<br />
208<br />
Ethyleneamines 0.248 2002<br />
209<br />
Epichlorohydrin 0.640 1999<br />
210<br />
Epoxy Resins 0.65 1999<br />
211<br />
3.3.10 Production Data<br />
Global production data for the most important monomers used for unsaturated<br />
epoxy resins are shown in Table 3.8.<br />
3.4 CURING<br />
3.4.1 Initiator Systems<br />
The epoxide group reacts with several substance classes. Only a few of the<br />
possible reactions are used for curing in practice. Curing agents of epoxy<br />
resins can be subdivided into three classes:<br />
1. Compounds with active hydrogens,<br />
2. Ionic initiators, <strong>and</strong><br />
3. Hydroxyl coupling agents.<br />
The most commonly used curing reaction is based on the polyaddition<br />
reaction, thereby opening the epoxide ring. The glycidyl group can be<br />
cured by amines <strong>and</strong> other nitrogen-containing compounds such as polyamides.<br />
Many of the amines effect curing at room temperature. This type<br />
of curing is called a cold curing.<br />
The reactivity of an epoxy compound with an amine depends on the<br />
structure of the compounds. The relative reaction rates of the secondary<br />
amine to the primary amine can be explained in terms of substitution effects.<br />
212 Anhydrides are active only at elevated temperatures. This type of<br />
curing is addressed as hot curing.
174 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
OH<br />
R NH 2<br />
+ CH 2 CH<br />
R NH CH 2 CH<br />
OH<br />
OH<br />
R<br />
NH CH 2<br />
O<br />
CH 2 CH<br />
CH<br />
R<br />
CH 2<br />
N<br />
CH 2<br />
CH<br />
CH<br />
OH<br />
O<br />
OH<br />
R OH + CH 2 CH<br />
R O CH 2 CH<br />
Figure 3.11: Reaction of the Glycidyl Group with an Amine <strong>and</strong> with a Hydroxy<br />
Group<br />
3.4.2 Compounds with Activated Hydrogen<br />
3.4.2.1 Amines<br />
Both primary <strong>and</strong> secondary amines can be used. From a chemical point of<br />
view, the active hydrogen attached to the nitrogen group effects an addition<br />
reaction, as the epoxide group is opened. The curing of the diglycidyl<br />
oligomer with a diamine occurs in three stages:<br />
1. Linear coupling of the oligomer,<br />
2. Formation of a branched structure, <strong>and</strong><br />
3. Crosslinking.<br />
The basic reaction between the glycidyl groups with a primary amine is<br />
shown in Figure 3.11. The first reaction in Figure 3.11 is the addition<br />
reaction of primary amine hydrogen with an epoxy group. The product<br />
of this reaction is a secondary amine. The secondary amine may react<br />
with another epoxy group to form a tertiary amine, as shown in the second<br />
reaction, Figure 3.11. Usually the secondary amine is less reactive than<br />
the primary amine. The ratio of the kinetic constants is approximately 1/2.<br />
Both reactions are autocatalyzed by OH groups formed during the process.<br />
The third reaction shown is the etherification reaction between epoxy<br />
functions <strong>and</strong> hydroxyl groups. In most systems, this reaction can
Compound<br />
Ethylene diamine<br />
Diethylenetriamine<br />
Triethylenetetramine<br />
Hexamethylene diamine<br />
Diethylaminopropylamine<br />
Isophorone diamine<br />
1,2-Diaminocyclohexane<br />
Bis-p-aminocyclohexylmethane<br />
Bisaminomethylcyclohexane<br />
Menthane diamine<br />
Table 3.9: Amines Suitable for Curing<br />
Remarks<br />
Epoxy Resins 175<br />
Fast curing, low viscosity<br />
Fast curing, low viscosity<br />
Fast curing, low viscosity<br />
Slower curing, needs elevated temperature,<br />
flexible materials<br />
Needs elevated temperature, good adhesive<br />
Needs elevated temperature,<br />
good potlife<br />
N-aminoethyl piperazine<br />
Fast curing<br />
Diaminodiethyl toluene<br />
Mixture of 2,6-diamino-3,5-diethyl<br />
toluene <strong>and</strong> 2,4-diamino-3,5-diethyl<br />
toluene<br />
m-Phenylene diamine<br />
Chemical resistant materials<br />
4,4 ′ -Diaminodiphenylmethane Chemical resistant materials<br />
3,3 ′ ,5,5 ′ -Tetraethyl-4,4 ′ -diamino Flame retardant 191<br />
diphenylmethane<br />
4,4 ′ -Diamino-3,3 ′ -dimethyl<br />
Cycloaliphatic diamine213, 214<br />
dicyclohexylmethane (DCM)<br />
1,5-Naphthalene diamine<br />
be neglected. However, it has been shown that this reaction takes place<br />
using 4,4 ′ -methylene bis(3-chloro-2,6-diethylaniline) (MCDEA) as curing<br />
catalyst. On the other h<strong>and</strong>, with 4,4 ′ -diaminodiphenylsulfone (DDS) <strong>and</strong><br />
4,4 ′ -methylenedianiline (MDA) as catalysts the etherification was not observed.<br />
109, 215<br />
Typical nitrogen compounds used for cold curing are shown in Tables<br />
3.9, <strong>and</strong> 3.10, <strong>and</strong> in Figures 3.12 <strong>and</strong> 3.13. There are many possibilities<br />
for formulating a curing system from primary <strong>and</strong> secondary amines,<br />
<strong>and</strong> also with tertiary amines.<br />
Tertiary amines catalyze the reaction. Other catalysts are complexes<br />
of boron trifluoride complexes, quaternary ammonium salts, thiocyano<br />
compounds, etc. Retarders are certain ketones <strong>and</strong> diacetone alcohol.
176 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 3.10: Polymeric Amines <strong>and</strong> Hetero Functional Amines<br />
Compound<br />
Remarks<br />
Poly(propylene oxide)diamine<br />
Trimercaptothioethylamine Optical applications23, 216<br />
Polymercaptopolyamines<br />
In combination with customary amine<br />
hardeners 217<br />
2,4-Diamino-4 ′ -methylazobenzene Optical applications 218<br />
(DMAB)<br />
4,4 ′ -Dithiodianiline Reversible crosslinking 219<br />
Dicy<strong>and</strong>iamide<br />
Common for adhesives<br />
4,4 ′ -Diaminodiphenylsulfone Chemical resistant materials<br />
bis(m-aminophenyl)methylphosphine<br />
191<br />
oxide (BAMPO)<br />
4,4 ′ -Methylene bis[3-chloro-<br />
67<br />
2,6-diethylaniline]<br />
Olefin oxide polyamine adducts Fast curing, low toxicity<br />
Glycidyl ether polyamine adducts Fast curing<br />
Diamide of dimerized linoleic acid For adhesives<br />
<strong>and</strong> ethlyene diamine<br />
Ketimines<br />
Low viscosity, long potlife,<br />
latent hardening catalysts<br />
2,5-Bis(aminomethyl)bicyclo[2.2.1] Norbornane diketimine 220<br />
heptane di(methylisopropyl<br />
ketimine)<br />
Substituted imidazolines, e.g., Wide range in stoichiometry<br />
2-ethyl-4-methylimidazole, 1-methylimidazole<br />
Sulfanilamide<br />
45, 221–223<br />
Polysilazane-modified polyamines Thermal resistant 224
Epoxy Resins 177<br />
H 2 N CH 2 CH 2 NH CH 2 CH 2 NH 2<br />
Diethylenetriamine<br />
H 2 N CH 2 CH 2 CH 2 CH 2 CH 2 CH 2 NH 2<br />
Hexamethylenediamine<br />
CH 3 CH 2<br />
N CH 2 CH 2 CH 2 NH 2<br />
CH 3 CH 2<br />
Diethylaminopropylamine<br />
H 2 N<br />
CH 3 CH 3<br />
C<br />
CH 3<br />
NH 2<br />
H 2 N<br />
CH 2<br />
CH 2<br />
N<br />
H<br />
Menthanediamine<br />
N-Aminoethyl piperazine<br />
Figure 3.12: Aliphatic Nitrogen Compounds for Curing: Diethylenetriamine,<br />
Hexamethylene diamine, Diethylaminopropylamine, Menthane diamine, N-aminoethyl<br />
piperazine
178 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
H 2 N<br />
NH 2<br />
NH 2<br />
H 2 N<br />
m-Phenyenediamine<br />
1,5-Napthalene diamine<br />
H 2 N<br />
O<br />
S<br />
O<br />
NH 2<br />
4,4’-Diaminodiphenylsulfone<br />
H 2 N<br />
CH 2 NH 2<br />
4,4’-Diaminodiphenylmethane<br />
Figure 3.13: Aromatic Nitrogen Compounds for Curing: m-Phenylene diamine,<br />
1,5-Naphthalene diamine, 4,4 ′ -Diaminodiphenylsulfone, 4,4 ′ -Diaminodiphenylmethane
Epoxy Resins 179<br />
Certain cyclic amines, such as 1,2-bis(aminomethyl)cyclobutane <strong>and</strong><br />
isomers of diaminotricyclododecane increase the pot life time. Polyamines<br />
<strong>and</strong> dicyanamide are preferably used for adhesive formulations.<br />
Phenolic hydroxyl groups exert autocatalysis at low conversions with<br />
respect to the ring opening of the epoxide group, thereby adding the amine<br />
groups. In the later stage of curing the amine groups are largely consumed<br />
<strong>and</strong> the phenolic hydroxyl groups start to react with the residual epoxide<br />
groups. 225 A suitable accelerator for adhesive formulations is 2,4,6-tris(dimethylaminomethyl)phenol.<br />
Most low molecular amines are toxic <strong>and</strong> also sensitive to the carbon<br />
dioxide in air. Therefore, the various adducts of the amines have been<br />
developed to mitigate this drawback.<br />
3.4.2.2 Ketimines<br />
Ketimines form the active amine structure by addition of water; thus they<br />
act as delayed-action catalysts.<br />
3.4.2.3 Amino Amides<br />
Amide-based compounds are used to achieve special properties <strong>and</strong> desired<br />
curing characteristics, such as lower toxicity, less sensitive final properties<br />
to the stoichiometry, lower peak temperatures for large castings. The active<br />
group in curing is not directly the amide group, but the attached primary<br />
<strong>and</strong> secondary amino groups present in the molecule. The amide group<br />
is helpful for achieving the other benefits, mentioned above. Examples<br />
for amino amides are adducts of polyamines with fumaric acid or maleic<br />
acid, or fatty acids. Similar to amines, in amine amides the reaction can be<br />
accelerated with boron trifluoride complexes, Mannich bases, etc.<br />
3.4.2.4 Metal salts<br />
Zirconium tetrachloride catalyzes effectively the nucleophilic opening of<br />
epoxide rings by amines. This has been used for the efficient synthesis<br />
of β-amino alcohols. 226 Zinc bromide <strong>and</strong> zinc perchlorate are also active<br />
in this manner. 227 However, it seems that this catalyst is not used for the<br />
curing of epoxy resins.
180 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Anhydride<br />
Table 3.11: Anhydrides for Hot Curing<br />
Remark/Reference<br />
Dodecenyl succinic anhydride Liquid<br />
Hexahydrophthalic anhydride<br />
3-Methyl-1,2,3,6-tetrahydrophthalic N,N-dimethylbenzylamine as accelerator<br />
228<br />
anhydride (MeTHPA)<br />
Hexahydro-4-methylphthalic<br />
anhydride<br />
Tetrahydrophthalic anhydride<br />
Methyltetrahydrophthalic anhydride<br />
Phthalic anhydride<br />
Methyl nadic anhydride<br />
Liquid<br />
HET anhydride<br />
Pyromellitic dianhydride (PMDA)<br />
5-(2,5-Dioxotetrahydrofuryl)-<br />
229<br />
3-methyl-3-cyclohexene-1,2-dicarboxylic<br />
anhydride<br />
(DMCDA)<br />
Glutaric anhydride Biodegradable Formulations 230<br />
Styrene-maleic anhydride<br />
Low molecular weight copolymers<br />
copolymers<br />
3.4.2.5 Phenols<br />
Bisphenol A is a main ingredient for the manufacture of glycidyl ethers.<br />
Polyfunctional phenols can be used to cure epoxy resins. This method<br />
did not find large commercial use, except in the development of highly<br />
chemically resistant coatings. The curing reaction is completely similar to<br />
the curing reaction of amines.<br />
Phenoplasts. Polyfunctional phenols can be applied as phenol/formaldehyde<br />
condensates of the novolak-type. In this field a wide variety has been<br />
examined, including phenolic adducts of chloromethylated diphenyl oxide,<br />
tetrabrominated bisphenol, <strong>and</strong> phenol adducts of poly(butadiene)<br />
3.4.2.6 Anhydride Compounds<br />
Typical anhydride compounds used for hot curing are shown in Table 3.11<br />
<strong>and</strong> in Figure 3.14. Most anhydrides need elevated temperatures to be<br />
active. The anhydride group is not active in the absence of acidic or basic
Epoxy Resins 181<br />
C 12 H 23<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
Dodecenylsuccinic anhydride<br />
Phthalic anhydride<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
Tetrahydrophthalic anhydride<br />
Hexahydrophthalic anhydride<br />
H 3 C<br />
CH<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
Methylnadic anhydride<br />
Pyromellithic anhydride<br />
Figure 3.14: Anhydrides for Hot Curing
182 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
catalysts; instead the anhydride group must be converted into the carboxyl<br />
group. This can be achieved by hydrolysis by natural occurring moisture,<br />
or by alcoholysis.<br />
The reaction of an anhydride is accelerated by a tertiary amine or by<br />
complexes of metal salts, such as ferric acetylacetonate. 231 The reaction<br />
of the anhydride group, as well as the acid group with the epoxide group,<br />
results in an ester linkage, with all the advantages <strong>and</strong> disadvantages of the<br />
ester link.<br />
Anhydrides are in some cases preferred over amines because they<br />
are less irritating to the skin, have longer pot life times, <strong>and</strong> low peak temperatures.<br />
Aromatic <strong>and</strong> cycloaliphatic anhydrides find wide applications<br />
for molding <strong>and</strong> casting techniques.<br />
3.4.2.7 Polybasic Acids<br />
The carboxyl group is capable of opening the epoxide group. Theoretically,<br />
the optimum stoichiometry is one acid group by one epoxide group. In<br />
practice an excess of acid is used.<br />
3.4.2.8 Polybasic Esters<br />
To obtain tough materials, the epoxides can be cured by the insertion reaction<br />
into ester groups. The curing agent is formed in-situ by the radical<br />
polymerization of N-phenylmaleimide <strong>and</strong> p-acetoxystyrene. 232 2,5-Dimethyl-2,5-bis(benzoylperoxy)hexane<br />
is suitable, because its decomposition<br />
temperature of 110°C is close to the desired cure temperature of 100°C.<br />
The two monomers copolymerize satisfactorily in the absence of the epoxy<br />
compound. The advantage of using the in-situ technique of polymerization<br />
is that the initial composition has low viscosity.<br />
The insertion mechanism is shown in Figure 3.15. Compared to<br />
epoxy systems cured with a phenol resin, the copolymer of N-phenylmaleimide<br />
<strong>and</strong> p-acetoxystyrene shows a significantly higher glass transition<br />
temperature.<br />
3.4.3 Coordination Catalysts<br />
Coordination catalysts consist of metal alkoxides, such as aluminum isopropyloxide,<br />
metal chelates, <strong>and</strong> oxides. Coordinative polymerization results<br />
in high molecular weight <strong>and</strong> stereospecific species.
Epoxy Resins 183<br />
O<br />
O<br />
H 3 C C O + CH 2 CH CH 2<br />
H 3 C<br />
O<br />
C<br />
O<br />
O CH 2 CH CH 2<br />
CH CH 2<br />
CH CH 2<br />
O<br />
N<br />
O<br />
O<br />
N<br />
O<br />
Figure 3.15: Insertion of the Epoxide into a Pendent Ester Group<br />
3.4.4 Ionic Curing<br />
3.4.4.1 Anionic Polymerization<br />
The anionic polymerization of epoxides can be initiated by metal hydroxides,<br />
<strong>and</strong> secondary <strong>and</strong> tertiary amines. The rate of curing is low in comparison<br />
to other curing methods. Therefore, anionic polymerization has not<br />
found wide industrial application. Moreover, the mechanical properties of<br />
the final materials are not satisfactory.<br />
3.4.4.2 Cationic Polymerization<br />
Cationic polymerization can lead to a crosslinking process if diepoxides<br />
are taken as monomers. Thus, a wide variety of compounds can be used<br />
catalytically as cationic curing initiators for epoxy resins that act at a high<br />
rate. Moreover, their low initial viscosities <strong>and</strong> fast curing make them good<br />
c<strong>and</strong>idates for rapid reactive processing.<br />
Cationic polymerization is initiated by Lewis acids. A lot of metal<br />
halogenides have been shown to be active, such as AlCl 3 , SnCl 4 , TiCl 4 ,<br />
SbCl 5 or BF 3 , but the most commonly used compound is boron trifluoride.<br />
In practice, boron trifluoride is difficult to h<strong>and</strong>le <strong>and</strong> the reaction runs<br />
too fast. Therefore, the compound is used in complexed form, e.g., as<br />
an ether complex or an amine complex. The strength of the ether <strong>and</strong><br />
amine complexes can be related to the base strength of the ether <strong>and</strong> amine,
184 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Compound<br />
Table 3.12: Latent Catalysts<br />
Reference<br />
N-Benzylpyrazinium hexafluoroantimonate<br />
233<br />
N-Benzylquinoxalinium hexafluoroantimonate<br />
233<br />
Benzyl tetrahydrothiophenium hexafluoroantimonate<br />
234<br />
o,o-Di-tert-butyl-1-piperidinylphosphonamidate<br />
235<br />
o-tert-Butyl-di-1-piperidinylphosphonamidate<br />
235<br />
o,o-di-tert-Butyl phenylphosphonate<br />
236<br />
o,o-Dicyclohexyl phenylphosphonate<br />
236<br />
respectively. Since the reactivity of a complex depends on the dissociation<br />
constant, some predictions on the activity of the complex can be made.<br />
Water or alcohols cause chain transfer reactions. The alcohol attacks<br />
the positively charged end of the growing polymer chain <strong>and</strong> forms an ether<br />
linkage or a hydroxyl group, respectively. The released proton can initiate<br />
the growth of another polymer chain. Diols <strong>and</strong> triols yield polymers with<br />
pendent hydroxyl groups. Therefore, diepoxides or higher functional epoxides<br />
are polymerized in the presence of diols or triols, etc.; branched <strong>and</strong><br />
crosslinked products may appear.<br />
In the cationic UV curing of an aliphatic epoxy compound it was<br />
observed that the polymerization rate decreased strongly after a conversion<br />
level of less than 10%. This effect was not caused by the glass transition<br />
temperature. However, the addition of 1,6-hexanediol (HD) raised the conversion<br />
at room temperature. 237<br />
There are photolatent <strong>and</strong> thermolatent catalyst systems. A great variety<br />
of those catalysts have been reviewed. 238 Besides the direct thermolysis<br />
of the initiator, also indirect methods are viable. Table 3.12 provides<br />
a list of latent catalysts.<br />
Spiroorthocarbonate. The cationic curing reaction of a bisphenol A-type<br />
epoxy resin in the presence of a spiroorthocarbonate can be performed with<br />
borontrifluoride dietherate. The spiroorthocarbonate undergoes a double<br />
ring opening reaction. 239 The conversion of the epoxy groups increases as<br />
the content of the spiroorthocarbonate increases.<br />
3,9-Di(p-methoxybenzyl)-1,5,7,11-tetra-oxaspiro[5.5]undecane, c.f.<br />
Figure 3.16 as spiroorthocarbonate, can be synthesized by the reaction of<br />
2-methoxybenzyl-1,3-propanediol with dibutyltin oxide.<br />
Differential scanning calorimetry shows two peaks that are attributed
Epoxy Resins 185<br />
H 3 C<br />
O O<br />
O O CH 3<br />
O O<br />
3,9-Di(p-methoxy-benzyl)-1,5,7,11-tetra-oxaspiro(5,5)undecane<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
3,23-Dioxatrispiro[tricyclo[3.2.1.0]octane-6,5’-<br />
1,3-dioxane-2’2"-1,3-dioxane-5",7’"-tricyclo[3.2.1.0octane]<br />
Figure 3.16: 3,9-Di(p-methoxybenzyl)-1,5,7,11-tetra-oxaspiro[5.5]undecane<br />
<strong>and</strong> 3,23-dioxatrispirotricyclo[3.2.1.0[2.4]]octane-6,5 ′ -1,3-dioxane-2 ′ 2 ′′ -<br />
1,3-dioxane-5 ′′ ,7 ′′′ -tricyclo[3.2.1.0[2.4]octane]<br />
to the polymerization of the epoxy group, <strong>and</strong> to the copolymerization of<br />
the spiroorthocarbonate with epoxy groups or homopolymerization, respectively.<br />
Copolymers containing a spiroorthocarbonate are capable of<br />
yielding a hard, non-shrinking matrix resin. Examples of these copolymers<br />
include a 2,3,8,9-di(tetramethylene)-1,5,7,11-tetraoxaspiro[5.5]undecane<br />
spiroorthocarbonate, <strong>and</strong> 3,23-dioxatrispirotricyclo[3.2.1.0[2.4]]octane-<br />
6,5 ′ - 1,3-dioxane-2 ′ 2 ′′ -1,3-dioxane-5 ′′ ,7 ′′′ -tricyclo[3.2.1.0[2.4]octane] <strong>and</strong><br />
cis,cis-, cis,trans-, <strong>and</strong> trans,trans-configurational isomers of 2,3,8,9-di-<br />
(tetramethylene)-1,5,7,11-tetraoxaspiro[5.5]undecane.<br />
These spiroorthocarbonates were determined to undergo an expansion<br />
of 3.5% during homopolymerization <strong>and</strong> demonstrated acceptable cytotoxicity<br />
<strong>and</strong> genotoxicity properties. These properties make them promising<br />
components of composite resin matrix materials. 20<br />
Trifluoromethanesulfonic acid salts. Triflic acid, i.e., trifluoromethanesulfonic<br />
acid, CF 3 SO 3 H is a known strong acid. Lanthanide triflates<br />
are Lewis acids <strong>and</strong> they maintain their catalyst activity even in aqueous<br />
solution. The strong electronegativity of the trifluoromethanesulfonate anion<br />
enhances the Lewis acid character of the initiator. Therefore, lanthanide<br />
triflates are excellent catalysts in the ring opening of the epoxy compounds.<br />
240
186 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Phosphonic Acid Esters. Phenylphosphonic esters decompose into phenylphosphonic<br />
acid <strong>and</strong> the corresponding olefins at 150 to 170°C. In the<br />
presence of ZnCl 2 they can initiate a cationic polymerization of glycidyl<br />
phenyl ether (GPE) to molecular weights up to 2000 to 7000 Dalton. 236<br />
Examples are o,o-di-1-phenylethyl phenylphosphonate, o,o-di-tertbutyl<br />
phenylphosphonate, <strong>and</strong> o,o-dicyclohexyl phenylphosphonate. These<br />
compounds can be synthesized from phenylphosphonic dichloride <strong>and</strong> the<br />
corresponding alcohols.<br />
Phosphonamidates. Phosphonamidates are thermally latent initiators,<br />
suitable for the polymerization of epoxides. 235 These compounds, such<br />
as o,o-di-tert-butyl-1-piperidinylphosphonamidate <strong>and</strong> further o-tert-butyl-di-1-piperidinylphosphonamidate<br />
can be synthesized from phosphorus<br />
oxychloride <strong>and</strong> piperidine in the presence of triethylamine, followed by<br />
the reaction with tert-butyl alcohol in the presence of sodium hydride. No<br />
polymerization of epoxide resins occurs below 110°C, whereas the curing<br />
proceeds rapidly above 110°C. At room temperature a mixture of epoxide<br />
<strong>and</strong> phosphonamidate is stable for months.<br />
3.4.5 Photoinitiators<br />
Photoinitiation is one of the most efficient methods for achieving very fast<br />
polymerization. Often the reaction can be completed within less than one<br />
second. 241 Curing with ultraviolet light has been developed for the coating<br />
area, printing inks <strong>and</strong> adhesives. The mechanism of photo curing consists<br />
mostly of a cationic photopolymerization of epoxides. The kinetics of the<br />
photoinduced reactions can be monitored by differential photocalorimetry.<br />
242 The major drawback of differential photocalorimetry is the rather<br />
long response time in comparison to the curing rate.<br />
The well-known use of radical generating photoinitiators in vinylcontaining<br />
systems is not applicable in pure epoxy systems. There is an<br />
exception when the epoxide resin is mixed with a vinyl monomer that bears<br />
the hydroxyl functionality or the amide functionality. The radical generating<br />
photoinitiator reacts then with the vinyl monomer. 243<br />
Common photoinitiators for epoxy systems are shown in Table 3.13.<br />
In the photoinduced curing of epoxides, the propagating polymer<br />
cations cannot deactivate one another, but require a deactivation by another<br />
species present in the polymerization mixture. Therefore, after the light
Compound<br />
Table 3.13: Photoinitiators for Epoxides<br />
Epoxy Resins 187<br />
Reference<br />
Aryl diazonium tetrafluoroborates<br />
4,4-Bis(N,N-dimethyl-N-(2-ethoxycarbonyl-1-propenyl)-<br />
244<br />
ammonium hexafluoro antimonate)benzophenone<br />
Calixarene derivatives<br />
245<br />
9-Fluorenyl tetramethylene sulfonium hexafluoroantimonate<br />
246<br />
Cyclopentadiene-Fe-arene hexafluorophosphate<br />
247<br />
is switched off, a pronounced postpolymerization reaction can be monitored.<br />
248 The conversion in the dark may contribute up to 80% of the total<br />
curing process. The overall polymerization quantum yield reaches ca. 200<br />
mol per photon.<br />
It has been shown that polyglycols, i.e., polyols from 1,2-diols, slow<br />
down the cationic polymerization, whereas polyols made from 1,4-diols do<br />
not show this effect. 234 Also the addition of small amounts of crown ethers<br />
(12-crown-4 ether) retards the polymerization. This behavior is attributed<br />
to complexes that are formed only with glycol-like structures that reduce<br />
the effective concentration of cations available to initialize the polymerization.<br />
3.4.5.1 Aryl Diazonium Tetrafluoroborates<br />
The azo group in aryl diazonium tetrafluoroborates decomposes on ultraviolet<br />
radiation into the aromatic compound, nitrogen <strong>and</strong> boron trifluoride.<br />
The latter compound initiates a cationic polymerization of the epoxide resin.<br />
The evolution of nitrogen limits the applications to thin films.<br />
3.4.5.2 Aryl Salts<br />
Other efficient photoinitiators are based on the photolysis of diaryliodonium<br />
<strong>and</strong> triarylsulfonium salts, that when decomposed liberate strong<br />
Brønsted bases. These bases initiate the cationic polymerization.<br />
It has been shown that diaryliodonium hexafluoroantimonate initializes<br />
photochemically the cationic copolymerization of 3,4-epoxycyclohexylmethyl-3<br />
′ ,4 ′ -epoxycyclohexane carboxylate <strong>and</strong> triethylene glycol methylvinyl<br />
ether. 249 Epoxy-functionalized silicones can be synthesized by
188 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
S<br />
Thioxanthone<br />
Anthracene<br />
Figure 3.17: Thioxanthone, Anthracene<br />
rhodium-catalyzed, chemoselective hydrosilation of vinyl ethers with siloxanes<br />
or silane. 250<br />
Epoxidized soyabean oil accelerates the crosslinking reaction of aromatic<br />
diepoxides in the presence of a triarylsulfonium photoinitiator. 251<br />
The photoinitiated copolymerization leads within seconds to a fully cured<br />
insoluble material showing increased hardness, flexibility, <strong>and</strong> scratch resistance.<br />
In interpenetrating networks, constructed by vinyl polymers <strong>and</strong> epoxides<br />
by photo curing, a mixture of a radically decomposing photoinitiator<br />
<strong>and</strong> a cationic photoinitiator is used. Examples are a mixture of a hydroxyphenylketone<br />
<strong>and</strong> a diaryliodonium hexafluorophosphate salt. During<br />
the UV curing of a mixture of acrylate <strong>and</strong> epoxide monomers, the epoxides<br />
react slower than acrylates. 173 The low efficiency of the initiation<br />
process is caused by the low ultraviolet absorbance of cationic photoinitiators.<br />
However, photosensitizers can improve the performance.<br />
Combinations of photo curing <strong>and</strong> thermal curing in interpenetrating<br />
networks of a vinyl polymer <strong>and</strong> an epoxide are possible. Such a combination<br />
of crosslinkable resins allows the partial or complete cure of each<br />
component independent of the other. 252<br />
3.4.5.3 Photosensitizers<br />
Photosensitizers can be used to improve characteristics of photo curing for<br />
pigmented materials. These photosensitizers exhibit significant UV absorption<br />
in the near UV <strong>and</strong> transfer the absorbed energy to a cationic photoinitiator.<br />
253 Examples for photosensitizers are anthracene <strong>and</strong> thioxanthone<br />
derivatives, such as 2,4-diethylthioxanthone, isopropylthioxanthone,<br />
c.f. Figure 3.17. Photoinitiators are iodonium salts that exhibit a compara-
Epoxy Resins 189<br />
CH 3<br />
H 3 C<br />
CH 2<br />
CH 2<br />
CH 3<br />
OH<br />
OH<br />
HO<br />
H 3 C<br />
CH 2 CH 2<br />
OH HO<br />
OH<br />
CH 2 CH 2 CH 3<br />
CH 3<br />
Figure 3.18: p-Methylcalix[6]arene<br />
tively low triplet state energy.<br />
3.4.5.4 Calixarenes<br />
Calixarenes are by-products in the phenol/formaldehyde condensation to<br />
prepare bakelite. They found attention for their application as surfactants,<br />
chemoreceptors, electrochemical <strong>and</strong> optical sensors, solid-phase extraction<br />
phases, <strong>and</strong> stationary phases for chromatography. 254<br />
The hydroxyl groups in calixarenes (c.f. Figure 3.18) can be protected<br />
with tert-butoxycarbonyl groups, trimethylsilyl groups, <strong>and</strong> cyclohexenyl<br />
groups, respectively. In this way the hydroxyl group does not react<br />
with an epoxide group. The phenol groups can be restored if a compound<br />
is present that generates acids photolytically. 245<br />
3.4.6 Derivatives of Michler’s Ketone<br />
4,4-Bis(N,N-dimethyl-N-(2-ethoxycarbonyl-1-propenyl)ammonium hexafluoro<br />
antimonate)benzophenone (MKEA) is synthesized from 4,4 ′ -bis(dimethylamino)benzophenone<br />
(Michler’s ketone) <strong>and</strong> ethyl α-(bromomethyl)acrylate,<br />
c.f. Figure 3.19. MKEA initiates cationic photopolymerization<br />
of cyclic ethers, like cyclohexene oxide (CHO) via a conventional addition
190 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
H 3 C<br />
N<br />
H 3 C<br />
O<br />
C<br />
CH 3<br />
N<br />
CH 3<br />
+<br />
Br<br />
CH 2 C CH 2<br />
C O<br />
O<br />
CH 2<br />
CH 3<br />
H 2 C<br />
O<br />
C CH 2<br />
CH 3<br />
N + O<br />
C<br />
CH 3<br />
N +<br />
CH 2 C CH 2<br />
C CH 3 CH 3 C O<br />
O<br />
-<br />
SBF 6<br />
-<br />
SBF 6<br />
O<br />
CH 2 CH 2<br />
CH 3 CH 3<br />
MKEA<br />
Figure 3.19: Synthesis of 4,4-Bis(N,N-dimethyl-N-(2-ethoxycarbonyl-1-propenyl)ammonium<br />
hexafluoro antimonate)benzophenone (MKEA)<br />
fragmentation mechanism. MKEA belongs to the group of addition-fragmentation<br />
catalysts.<br />
The mechanism of initiation of MKEA is shown in Figure 3.20. This<br />
initiator does not require supplementary free radical sources. It is suggested<br />
that radicals stemming from the photoinduced hydrogen abstraction<br />
participate in addition fragmentation reactions to yield reactive species capable<br />
of initiating cationic polymerization. 244<br />
Monomers with strong electron donors such as N-vinyl carbazole,<br />
isobutyl vinyl ether, <strong>and</strong> n-butyl vinyl ether undergo explosive polymerization<br />
upon illumination of light. In the case of cyclohexene oxide there<br />
is an induction period, owing to the trace impurities present, but afterwards,<br />
the polymerization proceeds readily.<br />
3.4.6.1 Photoinitiator Systems<br />
Visible light photoinitiator systems include an iodonium salt, a visible light<br />
sensitizer, <strong>and</strong> an electron donor compound. 20
Epoxy Resins 191<br />
R*<br />
+ H 2 C<br />
C<br />
CH 2<br />
CH 3<br />
N +<br />
O<br />
C<br />
CH 3<br />
O<br />
CH 2<br />
CH 3<br />
R*<br />
H 2 C<br />
C*<br />
CH 2<br />
CH 3<br />
N +<br />
O<br />
C<br />
CH 3<br />
O<br />
CH 2<br />
CH 3<br />
R*<br />
H 2 C<br />
C*<br />
CH 2<br />
+<br />
CH 3<br />
N*+<br />
O<br />
C<br />
CH 3<br />
O<br />
CH 2<br />
CH 3<br />
Figure 3.20: Mechanism of Initiation of 4,4-Bis(N,N-dimethyl-N-(2-ethoxycarbonyl-1-propenyl)ammonium<br />
hexafluoro antimonate)benzophenone (MKEA)
192 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Examples of useful aromatic iodonium complex salt photoinitiators<br />
include diaryliodonium hexafluorophosphates <strong>and</strong> diaryliodonium hexafluoroantimonates,<br />
such as (4-(2-hydroxytetradecyloxyphenyl))phenyliodoniumhexafluoroantimonate,<br />
(4-octyloxyphenyl)phenyliodonium hexafluoroantimonate<br />
(OPIA), <strong>and</strong> (4-(1-methylethyl)phenyl)(4-methylphenyl)-<br />
iodonium tetrakis pentafluorophenylborate. These salts are more thermally<br />
stable, promote faster reaction, <strong>and</strong> are more soluble in inert organic solvents<br />
than are other aromatic iodonium salts of complex ions. Diphenyl<br />
iodonium hexafluoroantimonate has a photoinduced potential greater than<br />
N,N-dimethylaniline.<br />
The second component in the photoinitiator system is the photosensitizer.<br />
Desirably, the photoinitiator should be sensitized to the visible<br />
spectrum to allow the polymerization to be initiated at room temperature<br />
using visible light. The sensitizer should be soluble in the photopolymerizable<br />
composition, free of functionalities that would substantially interfere<br />
with the cationic curing process, <strong>and</strong> capable of light absorption within<br />
the range of wavelengths between about 300 <strong>and</strong> about 1000 nanometers.<br />
Suitable sensitizers include compounds in the following categories:<br />
• α-Diketones<br />
• Ketocoumarins<br />
• Aminoarylketones<br />
• p-Substituted aminostyrylketones<br />
For applications requiring deep cure (e.g., cure of highly filled composites),<br />
it is preferred to employ sensitizers having an extinction coefficient<br />
below about 1000 lmol −1 cm −1 at the desired wavelength of irradiation<br />
for photopolymerization, or alternatively, the initiator should exhibit<br />
a decrease in absorptivity upon light exposure. Many of the α-diketones<br />
exhibit this property, <strong>and</strong> are particularly preferred for dental applications.<br />
A suitable photosensitizer is camphorquinone.<br />
The third component of the initiator system is an electron donor<br />
compound. The electron donor compound should be soluble in the polymerizable<br />
composition. Further, suitable compatibility <strong>and</strong> interplay with<br />
the photoinitiator <strong>and</strong> the sensitizer <strong>and</strong> other properties, like shelf stability,<br />
should be fulfilled. The donor is typically an alkyl aromatic polyether<br />
or an alkyl, aryl amino compound wherein the aryl group is optionally substituted<br />
by one or more electron withdrawing groups. Examples of suitable<br />
electron withdrawing groups include carboxylic acid, carboxylic acid ester,
Epoxy Resins 193<br />
ketone, aldehyde, sulfonic acid, sulfonate, <strong>and</strong> nitrile groups.<br />
In practice, the following compounds find application:<br />
4,4 ′ -Bis(diethylamino)benzophenone,<br />
4-Dimethylaminobenzoic acid (4-DMABA),<br />
Ethyl-4-dimethylamino benzoate (EDMAB),<br />
3-Dimethylaminobenzoic acid (3-DMABA),<br />
4-Dimethylaminobenzoin (DMAB),<br />
4-Dimethylaminobenzaldehyde (DMABAL),<br />
1,2,4-Trimethoxybenzene (TMB), <strong>and</strong><br />
N-Phenylglycine (NPG).<br />
3.4.7 Epoxy Systems with Vinyl Groups<br />
Besides pure epoxy systems, mixed systems such as epoxy acrylates are<br />
in use. These systems can be cured with radical photoinitiators. Examples<br />
for such initiators are 2-benzyl-2-dimethylamino-1-(4-morpholinophenyl)-<br />
butan-1-one (BDMB), 2-methyl-1-[4-(methylthio)phenyl]-2-morpholinopropan-1-one<br />
(TPMK), 2,2-dimethoxy-1,2-diphenylethan-1-one (BDK),<br />
<strong>and</strong> hydroxy-2-methyl-1-phenyl-propanone. 255<br />
3.4.8 Curing Kinetics<br />
There are various methods to investigate the kinetics of curing, including<br />
1. Viscometry,<br />
2. Differential scanning calorimetry,<br />
3. Modulated differential scanning calorimetry,<br />
4. Dielectric analysis,<br />
5. Dynamic mechanical analysis,<br />
6. In-situ Fourier transform infrared spectroscopy, <strong>and</strong><br />
7. Fluorescence response.<br />
3.4.8.1 Viscometry<br />
In the course of curing, the crosslinking density <strong>and</strong> the viscosity as well<br />
as the modulus of the resin system increase. The viscoelastic properties<br />
can be measured in a torsional motion. 256
194 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
3.4.8.2 Differential Scanning Calorimetry<br />
Differential scanning calorimetry is the only direct reaction rate method<br />
which operates in two modes: constant temperature or linear programmed<br />
mode. Several methods to evaluate the data obtained by differential scanning<br />
calorimetry are available. 257 The isoconversional method 258 is frequently<br />
used to calculate the energies of activation <strong>and</strong> evaluating the dependence<br />
of the effective activation energy on the extent of conversion. 259<br />
Relations are available between the degree of conversion, the time<br />
dependence of the conversion, <strong>and</strong> the direct measurable parameters, i.e.,<br />
viscometry, differential scanning calorimetry <strong>and</strong> dynamic mechanical analysis.<br />
The equation is always second-order although the coefficients to this<br />
equation are different for the individual methods. The DSC technique becomes<br />
insensitive at conversions shortly after the gel point. 260 However,<br />
changes in the heat capacity can be indicators of the onset <strong>and</strong> the finishing<br />
of the vitrification. 214<br />
Differential scanning calorimetry allows statements concerning the<br />
reaction mechanism of curing. The ring opening reaction between phenyl<br />
glycidyl ether <strong>and</strong> aniline was investigated by DSC. The reaction resembles<br />
the diepoxy-diamine cure mechanism. However, it was detected that<br />
besides that from the epoxy ring opening reaction, another exothermic process<br />
at the last stages of the reaction takes place. It was concluded that the<br />
reaction of epoxy ring opening by aniline occurs by two concurrent pathways,<br />
261, 262 an uncatalyzed one <strong>and</strong> an autocatalyzed one.<br />
3.4.8.3 Temperature Modulated Differential Scanning Calorimetry<br />
In temperature modulated differential scanning calorimetry (TMDSC), the<br />
sample is subjected to a sinusoidal temperature change. The instruments<br />
are called differential AC-calorimeters. This particular method can measure<br />
the storage heat capacity <strong>and</strong> the loss heat capacity, i.e., the reversible<br />
part of heat that can be withdrawn again by cooling, <strong>and</strong> a part of heat<br />
consumed by chemical reaction. A complex heat capacity with a real part<br />
(storage heat capacity) <strong>and</strong> an imaginary part (loss heat capacity) can be<br />
defined. 263 The treatment is similar to other complex modules in mechanics.<br />
During the curing, the glass transition temperature rises steadily.<br />
The reaction induced vitrification takes place when the glass transition<br />
temperature rises above the curing temperature. This transition can be fol-
Epoxy Resins 195<br />
lowed simultaneously with the reaction rate in TMDSC.<br />
264, 265<br />
Modulated differential scanning calorimetry allows detecting of reaction<br />
induced phase separations. The apparent heat capacity changes, as<br />
phase separation occurs. The cloud point can be determined with optical<br />
microscopy, <strong>and</strong> there is a correspondence between the optical method<br />
<strong>and</strong> the calorimetry method.<br />
266, 267<br />
In an amine curing system, a complex<br />
formed from the primary amine <strong>and</strong> the epoxide was postulated that<br />
initiates the curing reaction. The reactions of the primary amine <strong>and</strong> the<br />
secondary amine with an epoxy-hydroxyl complex are comparatively slow<br />
<strong>and</strong> thus rate determining during the whole curing process.<br />
264, 268<br />
In an<br />
epoxy-anhydride system some complications have been elucidated. 269<br />
Temperature modulated DSC can be used with advantage during isothermal<br />
curing of semi-interpenetrating polymer networks. 270<br />
3.4.8.4 Dielectric Analysis<br />
Dielectric analysis 271 is based on the measurement of the dielectric permittivity<br />
ε ′ <strong>and</strong> the dielectric loss factor ε ′′ in the course of curing. The<br />
complex dielectric constant ε ∗ may be expressed by<br />
ε ∗ = ε ′ − iε ′′ (3.1)<br />
The permittivity is proportional to the capacitance <strong>and</strong> depends on<br />
the orientation polarization. The orientation polarization results from the<br />
change in the dipole moment due to the chemical reaction <strong>and</strong> also from<br />
the change of the concentration of dipoles due to the volume contraction<br />
during the curing reaction. The loss factor corresponds to the energy loss.<br />
Both dielectric <strong>and</strong> mechanical measurements are suitable techniques<br />
for monitoring the curing process. Also, phase-separation processes<br />
can be monitored by dielectric analysis, because dielectric measurements<br />
are sensitive to interfacial charge polarization. Dipolar relaxation indicates<br />
the vitrification through the α-relaxation process in both phases. 272 Further,<br />
dielectric sensor measurements have the advantage that they can be<br />
made in the laboratory as well as in-situ in the fabrication tool in a production<br />
line. 273 A relation between the dielectric response <strong>and</strong> other methods<br />
measuring the gel point has been established in epoxy systems. 214<br />
Dielectric analysis, in combination with other experimental techniques,<br />
can be used to establish a time-temperature-transition (TTT) diagram.<br />
The curing must be measured in a series of experiments at differ-
196 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
ent temperatures. In such a diagram gelation, vitrification, full cures, <strong>and</strong><br />
phase-separation are marked. 274<br />
A technique involving simultaneous dielectric <strong>and</strong> near infrared measurements<br />
has been used for monitoring the curing of blends of a diglycidyl<br />
ether bisphenol A epoxy resin with a 4,4 ′ -diaminodiphenylmethane hardener<br />
<strong>and</strong> various amounts of poly(methyl methacrylate) as modifier. 275<br />
3.4.8.5 In-Situ Fourier Transform Infrared Spectroscopy<br />
During the curing reaction, the appearance or disappearance of various<br />
characteristic infrared b<strong>and</strong>s can be monitored. This method yields more<br />
information than a single parameter, e.g., as obtained from a DSC measurement.<br />
However, there is more work needed to calibrate the system properly<br />
than in a DSC experiment. Multivariate analysis, in particular alternating<br />
least squares (ALS), allows calculation of the concentration profiles <strong>and</strong><br />
the spectra of all species involved in the reaction of curing epoxy resins. 276<br />
During curing, the intensity of the epoxy group, at 789 to 746 cm −1<br />
decreases. 277 For example, based on such experiments, in the curing of a<br />
dicyanate ester (1,1-bis(4-cyanatophenyl)ethane) with a bisphenol A epoxide,<br />
the formation of an oxazoline structure has been proposed. 278<br />
3.4.8.6 Fluorescence Response<br />
Fluorescence is a very sensitive <strong>and</strong> non-destructive technique to monitor<br />
the curing. The fluorescence response from chemical labels <strong>and</strong> probes<br />
enables the changes to be followed in the surroundings of the chemical<br />
label. In the curing process, the viscosity may change about six orders of<br />
magnitude.<br />
A change in the viscosity of the medium leads to a decrease in the<br />
non-radiative decay rate <strong>and</strong> consequently a change in the fluorescence<br />
quantum yield. The reaction medium acts as a thermal bath for the excited<br />
fluorescent molecule. When the monomers become fixed in forming<br />
a crosslinked polymer, a reduction of translational, rotational, <strong>and</strong> vibrational<br />
degrees of freedom in the bath takes place. Therefore, a reduction<br />
in the number of non-radiative deactivation pathways <strong>and</strong> an increase in<br />
fluorescence intensity occurs.<br />
1-Pyrenesulfonyl chloride (PSC) was used as a chemical label for<br />
silica epoxy interfaces, the surface coated with (3-aminopropyl)triethoxysilane,<br />
because it reacts easily with amine groups, yielding sulphonamide
Epoxy Resins 197<br />
C<br />
O OH<br />
CH 2<br />
H 3 C CH 3<br />
N<br />
S O<br />
NH 2<br />
DNS-EDA<br />
O<br />
CH 2<br />
NH<br />
9-Anthroic acid<br />
Figure 3.21: 9-Anthroic acid, 5-dimethylaminonaphthalene-1-(2-aminoethyl)-<br />
sulfonamide (DNS-EDA)<br />
derivatives. 279 Also 9-anthroic acid, its ester derivatives <strong>and</strong> 5-dimethylaminonaphthalene-1-(2-aminoethyl)sulfonamide<br />
(DNS-EDA), c.f. Figure<br />
3.21 are common fluorescence dyes.<br />
280, 281<br />
3.4.9 Thermal Curing<br />
By investigating the curing of a commercial epoxy prepolymer with imidazole<br />
curing agents, it has been verified that the cure schedule influences<br />
the properties of the end product. The highest thermal stability of the polymers<br />
can be achieved by isothermal cure schedules. Samples cured by a<br />
temperature program showed lower glass transition temperatures. In a series<br />
of temperature programmed curing experiments, a lower heating rate<br />
resulted in higher transition temperatures <strong>and</strong> superior thermal stability.<br />
The initial <strong>and</strong> postcure schedules are thus of critical importance for the<br />
final properties of the polymer. 282<br />
3.4.10 Microwave Curing<br />
Due to increasing application in the aerospace <strong>and</strong> microelectronics industries<br />
the dem<strong>and</strong> for accelerated curing has emerged. In particular, for the<br />
microelectronics industry, the curing of thermoset systems has become a<br />
bottleneck of the whole production process. Besides photo curing, curing<br />
with γ-rays <strong>and</strong> electron beams is an alternative.<br />
Microwave curing of materials has the potential to deliver several<br />
major advantages over conventional thermal processing. One of these is
198 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
a decrease in the time necessary for manufacture since another potential<br />
advantage is that the power is directed to the sample. The microwave energy<br />
is absorbed throughout the body of the material rather than relying<br />
on thermal conduction <strong>and</strong> convection. Therefore, the energy consumed is<br />
less than thermal curing.<br />
Experiments with the diglycidyl ether of bisphenol A <strong>and</strong> three types<br />
of curing agents, i.e., 4,4 ′ -Diaminodiphenylsulfone, 4,4 ′ -Diaminodiphenylmethane,<br />
<strong>and</strong> m-phenylene diamine with various energies of microwave<br />
energy showed that in comparison to thermal curing microwave curing is<br />
faster. The glass transition temperatures are somewhat lower in the case<br />
of the products cured with microwave technology in comparison to those<br />
cured by thermal methods. 283 However, the curing performance is strongly<br />
dependent on the curing agent used. 284 The interfacial shear strengths in<br />
those composites cured with microwave techniques are comparable with<br />
being thermally postcured. 285<br />
3.5 PROPERTIES<br />
Mechanical properties of epoxy resins can be correlated <strong>and</strong> traced back<br />
to the constituting monomers. The mechanical properties of epoxy resins<br />
depend on the flexibility of the segments <strong>and</strong> on the crosslinking density.<br />
Epoxy resins shrink in the course of curing less than vinyl resins.<br />
It is important to distinguish between the shrinkage that occurs before<br />
gelling <strong>and</strong> after gelling. Only a shrinkage that occurs after gelling<br />
results in residual stress in the final product.<br />
Epoxy resins can exhibit several thermal transition regions, depending<br />
on the chemical nature of the monomers. These transitions influence<br />
the curing. If a glass transition occurs during curing at the temperature applied,<br />
the individual reactive parts of the pendant molecules can no longer<br />
move sufficiently <strong>and</strong> the curing reaction freezes at this conversion. However,<br />
raising the temperature effects further curing.<br />
Cycloaliphatic epoxy resins have a low viscosity. The cured resins<br />
exhibit a high glass transition temperature. On the other h<strong>and</strong>, they exhibit<br />
low break elongation <strong>and</strong> toughness because of their high crosslinking density.<br />
Epoxy resins show good electrical properties. Of course, the electrical<br />
properties are affected by the moisture content. On the other h<strong>and</strong>,<br />
the resins can be made electrically conductive, by metal particles such as
Table 3.14: Epoxies Based on Hybrid <strong>Polymers</strong><br />
Compounds<br />
Epoxy Resins 199<br />
Remark/Reference<br />
Siloxane polymer with pendant epoxide rings<br />
286–288<br />
Epoxy polyurethane hybrid resins<br />
Maleimide-epoxy resins<br />
289<br />
silver <strong>and</strong> copper. Epoxy resins adhere by forming strong bonds with the<br />
majority of surfaces, therefore, an important application is in adhesives.<br />
Epoxy resins have excellent resistance to acids, bases, organic <strong>and</strong> inorganic<br />
solvents, salts, <strong>and</strong> other chemicals.<br />
3.5.1 Hybrid <strong>Polymers</strong> <strong>and</strong> Mixed <strong>Polymers</strong><br />
Hybrid polymers <strong>and</strong> mixed polymers are summarized in Table 3.14. These<br />
include silicone-epoxy hybrid polymers, urethane-epoxy hybrid polymers,<br />
<strong>and</strong> maleimide-epoxy polymers.<br />
3.5.1.1 Epoxy-Siloxane Copolymers<br />
A siloxane polymer with pendant epoxide rings on the side chain of<br />
the polysiloxane polymer backbone, when blended with diglycidyl bisphenol<br />
A ether <strong>and</strong> cured, increases the mobility of the crosslinked network<br />
<strong>and</strong> the thermal stability. Graft siloxane polymer with pendant epoxide<br />
rings can be synthesized by the hydrosilylation of poly(methylhydrosiloxane)<br />
with allyl glycidyl ether. 286<br />
Aminopropyl-terminated poly(dimethylsiloxane) blended in an epoxy<br />
resin shows an outst<strong>and</strong>ing oil <strong>and</strong> water repellency in coatings. 290 The<br />
peel strength of a pressure-sensitive adhesive affixed to the modified epoxy<br />
resin also decreases. Polyether/poly(dimethylsiloxane)/polyether triblock<br />
copolymers added in amounts of 5 ca. phr, efficiently reduce the static<br />
friction coefficient of the cured blends upon steel. 291<br />
Silsesquioxanes are organosilicon compounds with the general formula<br />
[RSiO 3/2 ] n , c.f. Figure 8.1, at page 323. Silsesquioxane (SSO) solutions<br />
were reacted with diglycidyl either of bisphenol A with 4-dimethylaminopyridine<br />
as initiator, to result in SSO-modified epoxy networks. The<br />
modification with SSO increased the elastic modulus in the glassy state.<br />
This is explained by an increase in the cohesive energy density. 292
200 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
3.5.1.2 Maleimide-Epoxy Resins<br />
Maleimide-epoxy resins are based on N-(p-carboxyphenyl)maleimide <strong>and</strong><br />
allyl glycidyl ether. 289 The resin can be cured thermally <strong>and</strong> is suitable as<br />
one component resin.<br />
3.5.2 Recycling<br />
3.5.2.1 Solvolysis<br />
The recycling of wastes of epoxy resins is very difficult, because of the<br />
inherent infusibility <strong>and</strong> insolubility of the materials. Often the composite<br />
materials contain reinforcing fibers, metals, <strong>and</strong> fillers. 293<br />
Efficient destruction of the organic material in composites can be<br />
achieved by thermolysis processes or by incineration processes. These<br />
methods yield considerable amounts of non-combustible residues or decomposition<br />
products that are not attractive for further use.<br />
Valuable recycled materials can be obtained by solvolysis methods.<br />
Here, the depolymerization products <strong>and</strong> reinforcing fibers can be retrieved.<br />
By glycolysis with diethylene glycol, the ester linkages of a bis epoxide<br />
(diglycidyl ether of bisphenol A) that is cured with a di anhydride,<br />
are cleaved. The transesterification is catalyzed by titanium n-butoxide.<br />
In the case of 70% glass fiber/epoxide-anhydride composites, the<br />
glass fibers can be recovered. The liquid depolymerization products may<br />
be converted to polyols, components for unsaturated polyester resins, etc.<br />
The glycolysis of amine cured epoxide resins shows no volatile nitrogen<br />
compounds. The most favored path of degradation is the decomposition<br />
of the ether linkage of bisphenol A to yield oligomers with phenol<br />
groups. 294 The separation of the phenolic compounds from the glycolysis<br />
products can be achieved by liquid-liquid extraction.<br />
The glycolysis products can be basically used as a polyol in production<br />
of polyurethane. However, the hydroxyl value is much too high for<br />
polyurethane production.<br />
It has been suggested to use the solvolysis products from epoxide<br />
resins in combination with other solvolysis products, e.g., solvolysis products<br />
from wastes from PET for semi interpenetrating networks based on<br />
PET hydrolyzate <strong>and</strong> epoxies. 295
Epoxy Resins 201<br />
3.5.2.2 Reworkable Epoxies for Electronic Packaging Application<br />
Epoxy resins show excellent longevity <strong>and</strong> resistance to ageing. This is due<br />
to the formation of an insoluble <strong>and</strong> infusible crosslinked network during<br />
the cure cycle. This property is sometimes seen as a drawback from the<br />
repairability st<strong>and</strong>point.<br />
During the manufacture of expensive electronic parts, such as multi<br />
chip modules, several chips are mounted onto one high density board. If<br />
one chip is damaged, then the whole board will become useless. The same<br />
is true if some special electronic parts in a board need to be modified because<br />
of progress in technology.<br />
Therefore, the availability of a reworkable material, that is, one that<br />
undergoes controlled network breakdown, exp<strong>and</strong>s the potential routes to<br />
repairing, replacing, or removing assembled structures <strong>and</strong> devices. Implementing<br />
reworkable materials early could exp<strong>and</strong> recycling concerns that<br />
could be faced in the near future.<br />
An effective solution is to use thermally reworkable epoxide resins<br />
for underfilling.<br />
296, 297<br />
In such systems, the cured epoxy network can be<br />
degraded by locally heating to a suitable temperature, <strong>and</strong> the faulty chip<br />
could be replaced.<br />
Commercial cycloaliphatic epoxides degrade at about 300°C. Epoxides<br />
with secondary or tertiary ester bonds (as shown in Figure 3.22)<br />
have been demonstrated to decompose at temperatures between 200°C <strong>and</strong><br />
300°C. 216, 298 The epoxides are cycloaliphatic compounds <strong>and</strong> can be basically<br />
derived by the esterification of cyclohexenoic acid with α-terpineol<br />
with subsequent epoxidation. Diepoxides with carbamate <strong>and</strong> carbonate<br />
groups 299 also degrade in this temperature range. In comparison to chemical<br />
degradation methods, heat to degrade the network can be localized<br />
more easily in the rework process, thereby allowing for more precise control<br />
over the region of the board that will be reworked.<br />
Instead of branched ester structures, ether structures, c.f. Figure<br />
3.22, bottom, are also suitable c<strong>and</strong>idates for thermolabile linkages in epoxides.<br />
231<br />
Thio links can be used to form a reversible network. 219 Further diepoxides<br />
connected via acetal links can be used for the introduction of reversible<br />
chemical links. 300 This type of network can be degraded in acidic<br />
solvents.
202 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
O<br />
O<br />
O<br />
O<br />
CH 3<br />
O<br />
O<br />
O<br />
O<br />
CH 3<br />
O<br />
O<br />
CH 3<br />
O<br />
O<br />
CH 3<br />
O<br />
O<br />
CH 3 O<br />
CH 3<br />
O<br />
CH 3<br />
O O<br />
CH CH2<br />
O<br />
1,2-Bis (2,3-epoxycyclohexyloxy)<br />
propane<br />
O CH 3 CH 3<br />
O<br />
C CH<br />
CH 3<br />
O<br />
O<br />
2-Methyl-2,4-bis (2,3-epoxycyclohexyloxy)<br />
pentane<br />
Figure 3.22: Epoxides with Thermally Cleavable Groups for Controlled Network<br />
Breakdown: Top Esters, Bottom Ethers. 1,2-Bis(2,3-epoxycyclohexyloxy)propane,<br />
2-Methyl-2,4-bis(2,3-epoxycyclohexyloxy)pentane
Epoxy Resins 203<br />
3.6 APPLICATIONS AND USES<br />
3.6.1 Coatings<br />
The largest applications of epoxy resins are in coatings. Epoxy resin coatings<br />
have excellent mechanical strength <strong>and</strong> adhesion to many kinds of<br />
surfaces. They are corrosion resistant <strong>and</strong> resistant to many chemicals.<br />
Coatings find applications in various paints, white ware, <strong>and</strong> automotive<br />
<strong>and</strong> naval sectors, for heavy corrosion protection of all kinds. Epoxy coating<br />
formulations are available both as liquid <strong>and</strong> solid resins. Epoxy acrylic<br />
hybrid systems are used as coatings for household applications, e.g., indoor<br />
<strong>and</strong> outdoor furniture <strong>and</strong> metal products.<br />
Waterborne coatings are dispersions of special formulations of the<br />
resins with suitable surfactants. These materials can be applied by electrodeposition<br />
techniques. Powders can be applied as coatings by fluidizedbed<br />
techniques.<br />
3.6.2 Foams<br />
Epoxy resins can be fabricated to make foams. Foamable compositions<br />
have been described from a novolak resin, an epoxy resin, <strong>and</strong> a blowing<br />
agent. Water can act as a blowing agent, especially when higher density<br />
foams are required. Novolak resins are typically suspended in an aqueous<br />
solution, that is the blowing agent. 301 Encapsulated calcium carbonate or<br />
anhydrous sodium bicarbonate are suitable blowing agents. 302 Phosphoric<br />
acid is used to catalyze the polymerization of resin <strong>and</strong> it also reacts with<br />
the carbonate core to generate a blowing gas to form voids.<br />
3.6.3 Adhesives<br />
Approximately 5% of total epoxy resin production is used in adhesive applications.<br />
Epoxide resin adhesives are formulated two-component systems<br />
that cure at room temperature, <strong>and</strong> as hot curing systems in the form<br />
of films <strong>and</strong> tapes. Among others, acrylates are suitable modifiers for epoxy<br />
adhesives.<br />
3.6.4 Molding Techniques<br />
Epoxy resins are used in all known reactive molding techniques. Non-reinforced<br />
articles can be molded with aluminum molds. This is used for
204 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
electrical coil covering, etc. In electronic industries various embedment<br />
techniques, i.e., casting <strong>and</strong> potting, <strong>and</strong> impregnation are important applications.<br />
Laminated sheets are used for the fabrication of printed circuit<br />
boards in the electronics industry.<br />
Pultrusion <strong>and</strong> lamination are common techniques. Laminated articles<br />
are also used in building constructions for concrete molds, honeycomb<br />
cores, reinforced pipes, etc. Epoxy resins are superior to polyesters where<br />
adhesion <strong>and</strong> underwater strength are important.<br />
3.6.5 Stabilizers for Polyvinyl Chloride<br />
Epoxy resins with monofunctional epoxy groups in the prepolymer are effective<br />
in stabilizing polyvinyl chloride against dehydrochlorination during<br />
processing <strong>and</strong> use, in comparison to tribasic lead sulphate. Lead-based<br />
stabilizers for polyvinyl chloride are mostly banned <strong>and</strong> only allowed for<br />
a few applications. For example, the replacement of lead-based stabilizers<br />
by epoxy stabilizers will improve the environmental toxicity of lead in<br />
water flowing through PVC pipes. 303<br />
3.7 SPECIAL FORMULATIONS<br />
3.7.1 Development of Formulations<br />
In practice, epoxy resins are composed of a wide variety of individual components.<br />
To obtain a composition with the desired properties, a great deal<br />
of know-how is required.<br />
A solid knowledge of the structure-property relationships can serve<br />
as a valuable tool for the art of formulation. 304<br />
On the other h<strong>and</strong>, there are methods that are helpful in the development<br />
of formulations. In particular, statistical methods can save time.<br />
An overview of such methods is given in the st<strong>and</strong>ard book of Box <strong>and</strong><br />
Hunter. 305 Instead, most studies on epoxy formulation are done by the<br />
“one variable at a time” method. This means that only one parameter of<br />
interest is changed while the other remaining parameters are kept constant.<br />
This strategy provides admittedly valuable information, however, it does<br />
not allow a good insight into mutual interactions of formulation parameters.<br />
The usefulness of statistical methods in the field of formulation of<br />
epoxy adhesives has been demonstrated in the literature. 306
Epoxy Resins 205<br />
3.7.2 Restoration Materials<br />
A variety of epoxy resins are used for the consolidation of stone monuments<br />
in an outdoor environment. For these applications good weathering<br />
resistance <strong>and</strong> sufficient penetration depth is m<strong>and</strong>atory.<br />
A suitable epoxy monomer for restoration materials is 3-glycidoxypropyltrimethoxysilane<br />
(GLYMO) <strong>and</strong> amine curing agent is (3-aminopropyl)triethoxysilane<br />
(ATS). This monomeric composition penetrates<br />
deep enough to exceed the maximum moisture zone <strong>and</strong> creeps beyond the<br />
damaged layers.<br />
The alkoxysilane groups are hydrolytically unstable <strong>and</strong> generate<br />
silanol groups which may crosslink with one another, <strong>and</strong> also form bonds<br />
to the hydroxyl groups present in the stone, thus anchoring the organic<br />
polymer onto the lithic matrix.<br />
307, 308<br />
The curing kinetics of hybrid materials prepared from diglycidyl<br />
ether of bisphenol A <strong>and</strong> GLYMO has been investigated using poly(oxypropylene)diamine<br />
as a hardener. 309 The total conversion of epoxy groups<br />
was found to decrease with increasing content of GLYMO. The experimental<br />
data scattered, which was attributed to an uncontrolled initial hydrolysis<br />
of GLYMO caused by the varying air humidity during the sample preparation.<br />
3.7.3 Biodegradable Epoxy-polyester Resins<br />
Biodegradable epoxy-polyester resins consist of polyesters with pendent<br />
epoxidized allyl groups. 230 These polyesters are synthesized from succinic<br />
anhydride <strong>and</strong> allyl glycidyl ether <strong>and</strong> butyl glycidyl ether with benzyltrimethylammonium<br />
chloride as catalyst.<br />
The butyl glycidyl ether acts as a diluent for the allyl functionalities,<br />
in order to reduce the amount of pendant allyl groups in the chain. The<br />
epoxidation of the polyesters is achieved by m-chloroperbenzoic acid. The<br />
epoxy-polyester resins can be cured with glutaric anhydride.<br />
3.7.4 Swellable Epoxies<br />
Hydrophilic polymers find applications in medicine <strong>and</strong> agriculture, owing<br />
to their biocompatibility. 310<br />
Crosslinked structures, prepared from sucrose <strong>and</strong> 1,4-butanediol diglycidyl<br />
ether (1,4-BDE) are hydrogels with water regain values of 30%. 311
206 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
The crosslinking is achieved with triethylamine or sodium hydroxide. Triethylamine<br />
gives rise to end-capped diethylamine groups. By this reaction<br />
the ethyl group is left behind as ethyl ether in the sucrose.<br />
The ring-opening polymerization of epoxy end-terminated poly(ethylene<br />
oxide) (PEO) can serve to synthesize crosslinked materials with an<br />
exceptional swelling behavior. 312 These gels have attracted interest for use<br />
as drug delivery platforms.<br />
3.7.5 <strong>Reactive</strong> Membrane Materials<br />
<strong>Reactive</strong> membrane materials can be prepared from 2-hydroxyethyl methacrylate<br />
<strong>and</strong> glycidyl methacrylate by radical photopolymerization.<br />
Enzymes, such as cholesterol oxidase, can be directly immobilized<br />
on the membrane by the reaction of the amino groups of the enzyme <strong>and</strong><br />
the epoxide groups of the membrane. The immobilization improves the pH<br />
stability of the enzyme as well as its thermal stability. The immobilized<br />
enzyme activity remains quite stable. 313<br />
Poly(2-hydroxyethyl methacrylate) membranes can be also activated<br />
by direct treatment with epichlorohydrin. On such materials poly(L-lysine)<br />
could be immobilized. 314 Such a membrane with immobilized poly(Llysine)<br />
can be utilized as an adsorbent for DNA adsorption experiments.<br />
3.7.6 Controlled-release Formulations for Agriculture<br />
In order to introduce pendant dichlorobenzaldehyde functionalities as acetals,<br />
the epoxide functionalities in linear <strong>and</strong> crosslinked poly(glycidyl<br />
methacrylate) are hydrolyzed to diol groups. In the second step the pendant<br />
diol groups in the polymers are acetalized by dichlorobenzaldehyde. 315 Dichlorobenzaldehyde<br />
is a bioactive agent that is slowly released under various<br />
conditions.<br />
3.7.7 Electronic Packaging Application<br />
In flip-chip manufacturing, filled polymers serve as underfilling. Underfilling<br />
is the plastic material which is inserted in the gap between integrated<br />
circuit <strong>and</strong> the substrate. The gap is approximately 50 to 75 µm wide. The<br />
underfilling is used to couple the chip <strong>and</strong> the substrate mechanically. It decreases<br />
the residual stress in the solder joints caused by thermal expansion.
Epoxy Resins 207<br />
The materials used for underfilling should have good wetting characteristics,<br />
significant adhesion, high conductivity, <strong>and</strong> should not form voids.<br />
The prevention of void formation is essential for thermal conductivity. Low<br />
viscosity of the monomeric resin is essential to achieve void-free underfillings.<br />
A resin with a lower viscosity allows the addition of a greater amount<br />
of filler. The viscosity of a benzoxazine resin can be reduced by the incorporation<br />
of a low-viscosity epoxy resin. The benzoxazine resin imparts a<br />
low water uptake, a high char yield, <strong>and</strong> mechanical strength. The epoxy<br />
resin reduces the viscosity of the mixture <strong>and</strong> results in higher crosslinking<br />
density <strong>and</strong> improved thermal stability of the material. A melt viscosity of<br />
about 0.3 Pas at 100°C can be achieved. 316<br />
3.7.8 Solid Polymer Electrolytes<br />
The interest in solid polymer electrolytes arises from the possibility of applications<br />
of polymer ionic conductors in energy storage systems, electrochromic<br />
windows, <strong>and</strong> fuel cells or sensors operating from subambient to<br />
moderate temperatures. 317<br />
Hosts for solid polymer electrolytes are poly(ethylene oxide) (PEO),<br />
segmented polyurethanes with poly(ethylene oxide)/ poly(dimethylsiloxane)<br />
318 <strong>and</strong> with poly(ethylene oxide)/perfluoropolyether 319 blocks, respectively,<br />
as well as crosslinked epoxy-siloxane polymer complexes.<br />
320, 321<br />
The copolymers are immersed in a liquid electrolyte (1 M LiClO 4 in propylene<br />
carbonate) to form gel-type electrolytes.<br />
Solvent-free solid polymer electrolytes are based on polyether epoxy<br />
crosslinked with poly(propylene oxide) polyamines. 322 The crosslinked<br />
polyether networks are doped with LiClO 4 . The network is prepared by<br />
mixing epoxy monomer, the curing agent dissolved in acetone <strong>and</strong> LiClO 4 .<br />
To obtain films the mixture is poured on plates <strong>and</strong> cured at elevated temperatures.<br />
The electric conductivity of the polymer electrolyte is dependent<br />
on interactions between ions <strong>and</strong> the host polymer.<br />
3.7.9 Optical Resins<br />
3.7.9.1 Lenses<br />
In comparison to glasses, plastics have low density, i.e., comparative low<br />
weight, are fragmentation-resistant <strong>and</strong> can be easily dyed. Therefore, optical<br />
materials made from organic polymers are attractive for optical ele-
208 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
ments such as lenses of eyeglasses <strong>and</strong> cameras. However, the refractive<br />
index of the st<strong>and</strong>ard resins is relatively small. Therefore, there is a need<br />
to use materials with high refractive index <strong>and</strong> low chromatic aberration.<br />
The introduction of sulfur into the monomers raises the refractive index.<br />
Sulfur-containing resins have a high refractive index, low dispersion,<br />
<strong>and</strong> a good heat stability. 23, 216 Components for epoxy resin with high refractive<br />
index are obtained from bis(3-mercaptophenyl)sulfone (BEPTPhS)<br />
<strong>and</strong> epichlorohydrin.<br />
A sulfur-containing curing agent is trimercaptotriethylamine<br />
(TMTEA) which can be obtained from triethanolamine. Besides sulfurcontaining<br />
epoxies, with tailor-made polyphosphazenes, refractive indices<br />
ranging from 1.60 to 1.75 can be achieved. 323<br />
3.7.9.2 Liquid Crystal Displays<br />
In liquid crystal displays (LCDs), control of the alignment of the liquid<br />
crystal (LC) molecules is one of the most important issues with respect<br />
to the quality of LCDs. The rubbing method does not satisfy the recent<br />
dem<strong>and</strong>s for alignment quality. The photoalignment method reduces contaminations<br />
that lower the contrast ratio <strong>and</strong> electrostatic buildup that can<br />
cause failure of thin film transistors. 324<br />
Nematic liquid crystalline materials can be aligned homogeneously<br />
on a photoreactive polymer film when exposed to linearly polarized light.<br />
Thermal stability <strong>and</strong> photostability of the alignment layer is a crucial parameter<br />
<strong>and</strong> the alignment layer must be transparent in the visible region<br />
for a display device. Certain photocrosslinkable polymer systems meet<br />
these dem<strong>and</strong>s. Derivatives of cinnamic ester <strong>and</strong> cinnamic acid are suitable<br />
c<strong>and</strong>idates for phototransformations. In particular, the anisotropic<br />
[2+2] cycloaddition of the cinnamate moiety can induce an irreversible<br />
alignment of a low molecular weight liquid crystal. <strong>Polymers</strong> with the<br />
chalcone group in the side chain react in a similar way. A chalcone-epoxy<br />
compound can be synthesized from 4,4 ′ -Dihydroxychalcone <strong>and</strong> epichlorohydrin<br />
in the same way as with bisphenol A. In this photoreactive epoxy<br />
oligomer, the photosensitive unsaturated carbonyl moieties are located in<br />
the main chain. For the polymerization of the epoxy groups, triarylsulfonium<br />
hexafluoroantimonate (TSFA) is a suitable photoinitiator.<br />
The photodimerization of the chalcone precedes the photopolymerization<br />
of the epoxy groups. Under continuous irradiation, the anisotropic
Epoxy Resins 209<br />
O<br />
HO<br />
C<br />
CH<br />
CH<br />
OH<br />
1,3-Bis-(4-hydroxy-phenyl)-propenone<br />
Figure 3.23: 4,4 ′ -Dihydroxychalcone<br />
photocrosslinked chain molecules can be frozen by the photopolymerization<br />
of the epoxy groups at both ends of the compound. Without a photoinitiator,<br />
the end groups of the oligomer are not fixed. Therefore, there are<br />
two kinds of photochemical reactions that enhance the photostability of the<br />
induced optical anisotropy. 24<br />
3.7.9.3 Holography<br />
Materials for high-resolution holograms, which can be used on holographic<br />
optical elements such as heads-up display, consist of a bisphenol-type epoxy<br />
resin <strong>and</strong> a radically polymerizable aliphatic monomer. A diaryliodonium<br />
salt <strong>and</strong> 3-ketocoumarin (KCD) are used as a complex initiator. The<br />
formation of the image is based on the radical polymerization of the monomer<br />
initiated by a holographic exposure, followed by the cationic polymerization<br />
of the epoxy resin by UV-exposure after post-exposure baking. 325<br />
3.7.9.4 Nonlinear Optical <strong>Polymers</strong><br />
Second-order nonlinear optical (NLO) polymeric materials are of interest<br />
because of their potential applications in integrated optical devices, such as<br />
waveguide electro-optic modulators, switches, <strong>and</strong> optical frequency doubling<br />
devices. The interest in these polymeric materials is mainly due to<br />
their large optical nonlinearities, low dielectric constants, <strong>and</strong> ease of production.<br />
For practical use, the poled polymers must possess large secondorder<br />
optical nonlinearities which should be sufficiently stable at ambient<br />
temperature for a long period of time.<br />
A high crosslinking density <strong>and</strong> stiffness makes interpenetrating networks<br />
attractive for such applications. The possibility of introduction of<br />
chromophores that impart the nonlinear optical properties is essential.
210 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
An example for an NLO active interpenetrating polymer network is<br />
an epoxy prepolymer <strong>and</strong> a phenoxy-silicon polymer. 4,4 ′ -Nitrophenylazoaniline<br />
(Disperse Orange 3) functionalized with crosslinkable acryloyl<br />
groups is incorporated into the epoxy prepolymer. The epoxy prepolymer<br />
forms a network through acryloyl groups which are reactive at high temperatures<br />
without the aid of any catalyst or initiator. The phenoxy-silicon<br />
polymer is based on an alkoxysilane dye made of (3-glycidoxypropyl)trimethoxysilane<br />
<strong>and</strong> Disperse Orange 3, <strong>and</strong> 1,1,1-tris(4-hydroxyphenyl)-<br />
ethane, as a multifunctional phenol. The two networks are formed simultaneously<br />
<strong>and</strong> separately at 200°C. 326<br />
Interpenetrating polymer networks based on crosslinked polyurethane/epoxy<br />
based polymer can be obtained by simultaneously crosslinking<br />
phenol-capped isocyanates with 2-hydroxypropyl acrylate <strong>and</strong> curing epoxy<br />
prepolymers. To each of these components phenylazo-benzothiazole<br />
chromophore groups are linked. The crosslinked polyurethane <strong>and</strong> the epoxy<br />
based polymer show glass transition temperatures of 140 <strong>and</strong> 178°C,<br />
respectively, whereas the interpenetrating network shows two T g ’s at 142<br />
<strong>and</strong> 170°C. Thin, transparent poled films of the crosslinked polymers can<br />
be prepared by spin-coating, followed by thermal curing <strong>and</strong> corona poling<br />
at 160°C. The polymers exhibit a long-term stability of the dipole alignment<br />
at 120°C. 327<br />
3.7.10 <strong>Reactive</strong> Solvents<br />
<strong>Polymers</strong> can be processed more easily by using solvents. The disadvantage<br />
the necessary removal of the solvent. This might be tedious <strong>and</strong> a<br />
time consuming step. Also, environmental hazards may arise. <strong>Reactive</strong><br />
solvents are those that polymerize after the molding process. In this case,<br />
no removal is necessary. Accordingly, intractable polymers can be processed<br />
by the utilization of reactive solvents. The polymers are dissolved<br />
in a liquid curable resin. Then the homogeneous solution is transferred into<br />
a mold. The curing of the reactive solvent takes place in the mold.<br />
In the course of curing, molecular weight of the resin increases. A<br />
phase separation <strong>and</strong> phase inversion are likely to take place. The dissolved<br />
polymer should become the continuous matrix, <strong>and</strong> the reactive solvent is<br />
dispersed as particles in the matrix. So the final properties of the system<br />
are dominated by the properties of the thermoplastic phase.<br />
The main advantage of this procedure is a lower processing temper-
Epoxy Resins 211<br />
ature because of decrease with viscosity. There is no need to remove the<br />
solvent which is bounded to the polymer.<br />
3.7.10.1 Poly(butylene terephthalate)<br />
Although poly(butylene terephthalate) can be relatively easily processed,<br />
a further improvement of the processing is required when a difficult flow<br />
length or mold geometry has to be mastered. 328<br />
3.7.10.2 Poly(phenylene ether)<br />
Poly(2,6-dimethyl-1,4-phenylene ether) (PPE) can be dissolved at elevated<br />
temperatures in an epoxy resin <strong>and</strong> the solution can be easily transferred<br />
into a mold or into a fabric. 329<br />
During the curing of epoxy resin, a phase separation <strong>and</strong> a phase<br />
inversion occurs. The originally dissolved PPE then becomes the continuous<br />
phase. The dispersed epoxy particles become an integral part of the<br />
system <strong>and</strong> act as fillers or as toughening agents, depending on the type of<br />
epoxy resin. An important parameter for the final physical <strong>and</strong> mechanical<br />
properties is the size of the dispersed particles.<br />
The size of the dispersed phase is governed by the competition between<br />
the coalescence of dispersed droplets, <strong>and</strong> the vitrification or gelation<br />
rate, respectively, induced by the curing process. For the coalescence,<br />
the viscosity of the system plays an important role which is dependent on<br />
the curing temperature. The viscosity can be further controlled by adding<br />
another thermoplastic material such as poly(styrene).<br />
Blends of poly(phenylene ether) <strong>and</strong> an epoxy resin cured with dicy<strong>and</strong>iamide<br />
materials show a two-phase morphology. To improve the uniformity<br />
<strong>and</strong> miscibility, triallyl isocyanurate (TAIC) can be used as an insitu<br />
compatibilizer. 330 Also the fracture toughness of the modified systems<br />
is improved by adding TAIC.<br />
3.7.11 Encapsulated Systems<br />
Photopolymerizable liquid encapsulants (PLE) for microelectronic devices<br />
may offer important advantages over traditional transfer molding compounds.<br />
A PLE is comprised of an epoxy novolak-based vinylester resin,<br />
fused silica filler, a photoinitiator, a silane coupling agent, <strong>and</strong> optionally<br />
of a thermal initiator. 331
212 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
3.7.12 Functionalized <strong>Polymers</strong><br />
The epoxy group can be used to functionalize various polymers, to achieve<br />
certain desired properties.<br />
3.7.12.1 Tougheners<br />
Vinylester-urethane hybrid resins (VEUH) can be toughened by functionalized<br />
polymers. 332 Suitable basic materials for toughening are nitrile rubber,<br />
hyperbranched polyesters, <strong>and</strong> core/shell rubber particles. These materials<br />
can be functionalized with vinyl groups, carboxyl groups, <strong>and</strong> epoxy<br />
groups.<br />
Toughness is improved in VEUH when the functional groups of the<br />
modifiers react with the secondary hydroxyl groups of a bismethacryloxy<br />
vinylester resin <strong>and</strong> with the isocyanate groups of the polyisocyanate compound.<br />
Functionalized epoxy <strong>and</strong> vinyl hyperbranched polymers are less<br />
efficient as toughness modifiers in comparison to functionalized liquid nitrile<br />
rubber. They show no adverse effect on the mechanical properties.<br />
3.7.13 Epoxy Resins as Compatibilizers<br />
Most polymers are not miscible with one another. This lack of miscibility<br />
results in poor properties of polymeric blends. However the properties can<br />
be improved by adding compatibilizers. Due to the inherent reactivity of<br />
the epoxy group, an interfacial chemical bonding can be achieved which<br />
results in small particle sizes of the blend. This enhances the properties of<br />
the blends. Some compatibilizers based on epoxy compounds are shown<br />
in Table 3.15.<br />
3.7.13.1 Polyamide Blends<br />
Blends of polyamide 6 <strong>and</strong> epoxidized ethylene propylene diene (e-EPDM)<br />
can improve the toughness of polyamide 6. The particle size of e-EPDM<br />
is much smaller than that of unepoxidized EPDM (u-EPDM) rubber in a<br />
polyamide 6 matrix. It is believed that the epoxy group in e-EPDM reacts<br />
with the polyamide 6 to form a graft copolymer. Thus an interfacial<br />
compatibilization takes place. 333<br />
Styrene/glycidyl methacrylate (SG) copolymers are miscible with<br />
syndiotactic poly(styrene) (s-PS). In blends of polyamide 6 (PA6) with<br />
syndiotactic poly(styrene), the epoxide units in the SG phase are capable
Epoxy Resins 213<br />
Table 3.15: Compatibilizers Based on Epoxy Compounds for Various<br />
<strong>Polymers</strong><br />
Polymer 1 Polymer 2 Compatibilizer<br />
PA6 PS Styrene/glycidyl methacrylate copolymers<br />
PA6 ABS Glycidyl methacrylate/ methyl methacrylate copolymers<br />
(GMA/MMA)<br />
PA6 PP Poly(ethylene) functionalized with maleic anhydride<br />
PBT PPE Low molecular weight epoxy compounds<br />
PBT SAN Terpolymers of methyl methacrylate, glycidyl<br />
methacrylate (GMA), <strong>and</strong> ethyl acrylate<br />
PA6 Polyamide 6<br />
PS Poly(styrene)<br />
PBT Poly(butylene terephthalate)<br />
ABS Acrylonitrile butadiene styrene (ABS) copolymers<br />
PP Poly(propylene)<br />
SPE Poly(phenylene ether)<br />
SAN Styrene/acrylonitrile copolymers<br />
of reacting with the PA6 end groups. Copolymers of styrene/glycidyl methacrylate<br />
are effective in reducing the s-PS domain size <strong>and</strong> improving the<br />
interfacial adhesion. The best compatibilization is found with a content of<br />
5% glycidyl methacrylate (GMA) in the SG copolymer. Both the strength<br />
<strong>and</strong> modulus of the blend are improved by the addition of the SG copolymers.<br />
However, a loss in toughness is observed at loadings of copolymer.<br />
The addition of SG copolymer to the blend has little influence on the crystallization<br />
behavior of the polyamide component. The crystallinity of s-PS<br />
is reduced. 334<br />
Blends of nylon 6 with acrylonitrile/butadiene/styrene (ABS) copolymers<br />
<strong>and</strong> with styrene/acrylonitrile copolymers (SAN) can be prepared<br />
using glycidyl methacrylate/methyl methacrylate (GMA/MMA) copolymers<br />
as compatibilizing agents. 335<br />
Known compatibilizers for blends of low density poly(ethylene)<br />
(LDPE) <strong>and</strong> polyamide 6 (PA6) are ethylene/acrylic acid copolymers<br />
(EAA), maleic anhydride functionalized polyethylenes, <strong>and</strong> an ethylene-<br />
/glycidylmethacrylate copolymer (EGMA). The effectiveness of EGMA<br />
as a reactive compatibilizer is comparable to that of the EAA copolymers.<br />
However the effectiveness is lower than that of poly(ethylene) functionalized<br />
with maleic anhydride. A possible reason is the reaction of the pendent
214 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
epoxy groups with the amide groups that attach the polyamide molecules<br />
together <strong>and</strong> hinder the dispersion in this way. 336<br />
In blends of poly(propylene) <strong>and</strong> polyamide 6, poly(ethylene) functionalized<br />
with maleic anhydride showed better compatibilization than<br />
glycidyl methacrylate. The compatibilizing effect of the PP-MA for the<br />
PP/Ny6 blends was more effective than poly(propylene) functionalized<br />
with glycidyl methacrylate. 337<br />
Glycidyl methacrylate copolymers are miscible with SAN. The epoxide<br />
unit can react with the polyamide end groups. The compatibilizer<br />
can form graft copolymers at the polyamide/SAN interface during melt<br />
processing. Incorporation of the compatibilizer does not significantly improve<br />
the impact properties of nylon 6/ABS blends.<br />
The direct mixing of polyamide <strong>and</strong> poly(propylene) leads to incompatible<br />
blends with poor properties. Poly(propylene) functionalized with<br />
glycidyl methacrylate can be used as a compatibilizer in the blends of PP<br />
<strong>and</strong> nylon 6. 338<br />
3.7.13.2 Poly(butylene terephthalate)<br />
Poly(butylene terephthalate) (PBT) <strong>and</strong> poly(phenylene ether) (PPE) can<br />
be compatibilized by low molecular weight epoxy compounds. 339 Terpolymers<br />
of methyl methacrylate, glycidyl methacrylate (GMA), <strong>and</strong> ethyl<br />
acrylate are effective reactive compatibilizers for blends of (Poly(butylene<br />
terephthalate) (PBT) with styrene/acrylonitrile copolymers (SAN) or ABS<br />
materials. 340 During melt processing, the carboxyl end groups of PBT react<br />
with epoxide groups of GMA to form a graft copolymer.<br />
In blends of poly(butylene terephthalate) with an ethene/ethyl acrylate<br />
copolymer (E/EA), which show the general features of uncompatibilized<br />
polymer blends, such as a lack of interfacial adhesion <strong>and</strong> a relatively<br />
coarse unstabilized morphology, no evidence of transesterification reaction<br />
was found. In contrast, blends containing both virgin <strong>and</strong> modified<br />
E/MA/GMA terpolymers show a complex behavior. Two competitive reactions<br />
take place during the melt blending:<br />
1. Compatibilization due to interfacial reactions between PBT chain<br />
ends <strong>and</strong> terpolymer epoxide groups, resulting in the formation of<br />
E/MA/GMA/PBT graft copolymer, <strong>and</strong><br />
2. Rapid crosslinking of the rubber phase due to the simultaneous<br />
presence of hydroxyl <strong>and</strong> epoxide groups on E/MA/GMA chains.
Epoxy Resins 215<br />
The competition reactions between compatibilization <strong>and</strong> crosslinking<br />
are dependent on the type of the terpolymer, since the modified E/-<br />
MA/GMA contains hydroxyl groups before mixing. The in-situ compatibilization<br />
reaction of the pendent epoxy groups with PBT causes the formation<br />
of E/MA/GMA hydroxyl groups. 341<br />
The concentration of carboxyl groups at the PBT chain ends influences<br />
the rate of compatibilization but not the final morphology. The lower<br />
the concentration, the slower the morphology development. Ternary blends<br />
of PBT/(E-MA-GMA/E-MA) exhibit a very fine morphology. Here the development<br />
of the morphology is mildly influenced by the crosslinking rate<br />
of the rubber phase caused by the shear rate in the mixing chamber. 342<br />
3.7.14 Surface Metallization<br />
Established methods for the metallization of a polymer surface are 343<br />
1. Electroless plating,<br />
2. Vacuum deposition or metal spraying, <strong>and</strong><br />
3. Coating using a metallic paint.<br />
A more recent method has been described that utilizes the reduction<br />
of metal ions incorporated directly in the polymer. It has been shown that<br />
cobalt or nickel ions integrated in an epoxy network could be reduced to<br />
the pure metal by dipping the film in an aqueous NaBH 4 solution. 229<br />
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4<br />
Phenol/formaldehyde Resins<br />
Phenolic resins are known as the oldest thermosetting polymers. They<br />
still have many industrial applications in sectors such as automotive, computing,<br />
aerospace, <strong>and</strong> building. Reviews concerning phenolic resins are<br />
given, for example, by Gardziella <strong>and</strong> by Burkhart. 1–3<br />
Phenolic resins are thermosetting resins produced by the condensation<br />
of a phenol with an aldehyde wherein water is produced as a byproduct.<br />
Typically, the phenol is phenol itself <strong>and</strong> the aldehyde is formaldehyde,<br />
but substituted phenols <strong>and</strong> higher aldehydes have been used to<br />
produce phenolic resins with specific properties such as reactivity <strong>and</strong> flexibility.<br />
The variety of phenolic resins available is quite large as the ratio of<br />
phenol to aldehyde, the reaction temperature, <strong>and</strong> the catalyst selected can<br />
be varied. 4<br />
Phenolic resins fall into two broad classes:<br />
1. Novolak resins,<br />
2. Resol resins.<br />
Resol resins are single stage resins <strong>and</strong> novolak resins are two-stage<br />
resins. Resol resins are typically produced with a phenol, a molar excess of<br />
formaldehyde, <strong>and</strong> an alkaline catalyst. The reaction is controlled to create<br />
a non-crosslinked resin that is cured by heat without additional catalysts to<br />
form a three-dimensional crosslinked insoluble, infusible polymer. In contrast,<br />
novolak resins are typically produced with formaldehyde, at molar<br />
excess of phenol, <strong>and</strong> an acid catalyst.<br />
241
242 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 4.1: Types of Novolak Resins<br />
Novolak Resin Type<br />
Ratio ortho:para<br />
High ortho novolak 75:25<br />
General-purpose novolak 45:55<br />
High para novolak 38:62<br />
Suitable acid catalysts include the strong mineral acids such as sulfuric<br />
acid, phosphoric acid, <strong>and</strong> hydrochloric acid as well as organic acid<br />
catalysts such as oxalic acid, p-toluenesulfonic acid, <strong>and</strong> inorganic salts<br />
such as zinc acetate or zinc borate.<br />
The reaction produces a thermoplastic polymer that can be melted<br />
but will not crosslink upon the application of heat alone. The resulting<br />
novolak thermoplastic resin can be crosslinked by the addition of a novolak<br />
curing agent.<br />
There are various types of novolak resins with different ortho-to-para<br />
ratios of the methylene linkages: high ortho novolak resins (HON), general-purpose<br />
novolak resins (GPN), <strong>and</strong> high para novolak resins (HPN).<br />
The characterization is listed in Table 4.1.<br />
Resol resins require no additional curing agents. They can be cured<br />
by heat reactive. However, they have a low shelf life. Curing for resols <strong>and</strong><br />
hexamine-cured novolaks proceeds at 150 to 200°C.<br />
4.1 HISTORY<br />
As early as in 1872, Baeyer ∗ reported about reactions of phenols <strong>and</strong> aldehydes<br />
that give resinous substances. In 1899, Arthur Smith patented phenol/formaldehyde<br />
(PF) resins to replace ebonite as electrical insulation. In<br />
1899, Arthur Smith filed patent application for a method for substituting<br />
ebonite, wood, etc. 5 In 1907 Baekel<strong>and</strong> † mixed phenol <strong>and</strong> formaldehyde<br />
<strong>and</strong> obtained phenol/formaldehyde resins. In 1907 he filed the first of 117<br />
patents on phenol/formaldehyde resin systems. 6<br />
Before he was engaged in phenolic resins, Baekel<strong>and</strong> worked on the<br />
development of copying papers. Such a product became famous under<br />
the name Velox. Formica was first produced by Herbert Faber <strong>and</strong> Daniel<br />
O’Conor as an electrical insulator in 1910. Formica is a composite that<br />
∗ Adolf von Baeyer, born in Berlin 1835, died in Starnberg 1917<br />
† Leo Hendrick Baekel<strong>and</strong>, born in Gent 1863, died 1944
Phenol<br />
Phenol/formaldehyde Resins 243<br />
Table 4.2: Phenolic Monomers<br />
Remark/Reference<br />
Phenol<br />
Most common<br />
Bisphenol A<br />
2,2-Bis(4-hydroxyphenyl)propane<br />
Bisphenol F<br />
Bis(4-hydroxyphenyl)methane<br />
Bisphenol B<br />
2,2-Bis(4-hydroxyphenyl)butane<br />
Resorcinol<br />
Cresols<br />
Methylphenols<br />
m-Cresol Photoresists 7<br />
p-Cresol Photoresists 7<br />
2-Cyclohexyl-5-methylphenol Photoresists 7<br />
Xylenols<br />
m-Aminophenol<br />
8<br />
m-Methoxyphenol<br />
8<br />
β-Naphthol<br />
Cardanol<br />
Cardol<br />
Aldehyde<br />
Table 4.3: Aldehyde-type Components<br />
Remark/Reference<br />
Formaldehyde<br />
Most common<br />
Paraformaldehyde<br />
9<br />
Butyraldehyde<br />
Hot-melt adhesives <strong>and</strong> as binders for<br />
non-wovens 10<br />
Glyoxal Improved optical properties 11<br />
Multihydroxymethyl ketones<br />
12, 13<br />
consists of layers of paper impregnated with phenolic <strong>and</strong> melamine resins.<br />
In 1952 the first long-playing records <strong>and</strong> singles were manufactured from<br />
polyvinyl chloride which replaced shellacs <strong>and</strong> phenolics previously used.<br />
4.2 MONOMERS<br />
Derivatives of phenol that are suitable for use for phenol/formaldehyde<br />
resins are listed in Table 4.2. They include bisphenol A, bisphenol B, resorcinol,<br />
cresols, <strong>and</strong> xylenols. Derivatives of formaldehyde that are suitable<br />
for use for phenol/formaldehyde resins are listed in Table 4.3. They<br />
include paraformaldehyde, acetaldehyde, propionaldehyde, butyraldehyde<br />
<strong>and</strong> glyoxal, trioxane, furfural, <strong>and</strong> furfurol.
244 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
CH 3<br />
CH 3<br />
+<br />
CH<br />
CH<br />
CH 2<br />
CH 3<br />
O<br />
CH 3<br />
C<br />
H + -H 2 O<br />
CH 3<br />
C O<br />
OH<br />
CH 3<br />
CH 3<br />
OH<br />
CH 3 C CH 3<br />
O<br />
Figure 4.1: Synthesis of Phenol <strong>and</strong> Acetone<br />
4.2.1 Phenol<br />
The peroxidation of cumene is the preferred route to phenol, accounting<br />
for over 90% of world production. The process which is also referred to as<br />
the Hock Process or Cumox Process, consists of<br />
1. Liquid-phase oxidation of cumene to cumene hydroperoxide<br />
(CHP), <strong>and</strong><br />
2. Decomposition of the concentrated CHP to phenol <strong>and</strong> acetone.<br />
The synthesis is shown in Figure 4.1. The main use of phenol is as<br />
a feedstock for phenolic resins, bisphenol A, <strong>and</strong> caprolactam. It is also<br />
used in the manufacture of many products including insulation materials,<br />
adhesives, lacquers, paint, rubber, ink, dyes, illuminating gases, perfumes,<br />
soaps, <strong>and</strong> toys.<br />
4.2.2 o-Cresol<br />
o-Cresol is used mostly as an intermediate for the production of pesticides,<br />
epoxy resins, dyes, <strong>and</strong> pharmaceuticals, but also as a component of disinfectants<br />
<strong>and</strong> cleaning agents. o-Cresol is readily biodegradable <strong>and</strong> has a
Phenol/formaldehyde Resins 245<br />
Table 4.4: Uses of Formaldehyde<br />
Chemical<br />
Phenol/formaldehyde resins<br />
urea/formaldehyde resins<br />
Wood adhesives<br />
Foundry materials<br />
Polyacetal resins<br />
1,4-Butanediol<br />
Methylene bis(4-phenyl isocyanate)<br />
Pentaerythritol<br />
Controlled-release fertilizers<br />
Melamine/formaldehyde resins<br />
Paraformaldehyde<br />
Chelating agents<br />
Herbicides<br />
Trimethylolpropane<br />
Pyridine chemicals<br />
Neopentyl glycol<br />
Nitroparaffin derivatives<br />
Textile chemicals<br />
Trimethylolethane<br />
low bioaccumulation or geoaccumulation potential.<br />
Approximately 60% of o-cresol is obtained from coal-tar <strong>and</strong> crude<br />
oil by using classical techniques such as distillation, stripping, <strong>and</strong> liquid-liquid<br />
extraction. The remaining 40% is obtained synthetically by the<br />
alkylation of phenol with methanol.<br />
4.2.3 Formaldehyde<br />
Formaldehyde is a basic industrial chemical. It is used for the production<br />
of a variety of chemicals, as shown in Table 4.4. Formaldehyde is a colorless,<br />
highly flammable gas that is sold commercially as 30 to 50% aqueous<br />
solutions.<br />
Formaldehyde is used predominantly in the synthesis of resins, with<br />
urea/formaldehyde resins, phenolic-formaldehyde resins, pentaerythritol,<br />
<strong>and</strong> other resins. About 6% of uses are related to fertilizer production.<br />
Formaldehyde find application in a variety of industries, including the medical,<br />
detergent, cosmetic, food, rubber, fertilizer, metal, wood, leather, petroleum,<br />
<strong>and</strong> agricultural industries. 14
246 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
H 3 C C CH 2 CH 2 (O CH 2 )n OH<br />
CH 2 O<br />
O<br />
H 3 C C CH 2 CH 2 (O CH 2 ) n-1<br />
OH<br />
Figure 4.2: Multihydroxymethylketones<br />
Table 4.5: Global Production/Consumption Data of Important Monomers<br />
<strong>and</strong> <strong>Polymers</strong> 15<br />
Monomer Mill. Metric tons Year Reference<br />
Formaldehyde 24 2003<br />
16<br />
Benzene 44 2003<br />
17<br />
Bisphenol A 2 1999<br />
18<br />
Phenol 6.4 2001<br />
19<br />
Phenolic resins 2.9 2001<br />
20<br />
Resorcinol 0.046 2002<br />
21<br />
4.2.4 Multihydroxymethylketones<br />
Multihydroxymethylketones are the reaction products of ketones with a<br />
large excess of formaldehyde. 13 They are used as reactive solvents for melamine<br />
<strong>and</strong> other applications, but also can act as a source of formaldehyde,<br />
because they will decompose back, as shown in Figure 4.2.<br />
A mixture of phenol in a multihydroxymethylketone produces a special<br />
type of a modified phenol/formaldehyde resin.<br />
4.2.5 Production Data of Important Monomers<br />
Production data of raw materials for phenolic resins are shown in Table 4.5.<br />
Only a minor part of the formaldehyde produced is consumed for making<br />
phenol resins. Bisphenol A is also used in other resin systems, mainly for<br />
epoxide resins.
Phenol/formaldehyde Resins 247<br />
4.2.6 Basic Resin Types<br />
4.2.6.1 Novolak Resins<br />
A novolak resin is a precondensate consisting of at least one phenol, or a<br />
phenol derivative, <strong>and</strong> at least one aldehyde. Novolak resins are used, for<br />
example, in rubber preparations which serve the production of belts, tubes<br />
<strong>and</strong> tires.<br />
These resins can reinforce the rubber preparations by contributing<br />
hardness <strong>and</strong> high moduls with low deformation after curing. The reinforcement<br />
is explained by the formation of a three-dimensional network<br />
within the rubber upon curing.<br />
4.2.6.2 Resol Resins<br />
Phenolic resol resins are typically made by condensation polymerization<br />
of phenol <strong>and</strong> formaldehyde in the presence of a catalyst at temperatures<br />
between 40°C <strong>and</strong> 100°C. An alkaline catalyst is essential. If an acid catalyst<br />
would be used, an uncontrolled curing during the preparation of the<br />
prepolymer would occur. On the other h<strong>and</strong>, in principle, curing of the<br />
resol prepolymer could be achieved by acidifying.<br />
Due to the low yield of the phenol <strong>and</strong> formaldehyde condensation<br />
under the normal reaction conditions, a typical resol resin contains a high<br />
percentage of free monomers, i.e., phenol <strong>and</strong> formaldehyde. These free<br />
monomers are volatile <strong>and</strong> highly toxic. Reducing the level of free monomers<br />
in such resins, thus reducing their emissions into the environment<br />
during application processes, has been one of the most heavily researched<br />
areas by both phenolic resin producers <strong>and</strong> resin users for many years. 22<br />
Resol refers to phenolic resins that contain useful reactivity, as opposed<br />
to the cured resins. At this stage, the product is fully soluble in one<br />
or more common solvents, such as alcohols <strong>and</strong> ketones, <strong>and</strong> is fusible at<br />
less than 150°C.<br />
4.2.7 Specialities<br />
4.2.7.1 Modification with Lignin<br />
Lignin (poly(phenylpropane) units) from waste black can be used for a partial<br />
substitution of the phenol in a phenol/formaldehyde resin. The amount
248 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
C 4 H 9<br />
S H 2 C<br />
OH<br />
OH HO C 4 H 9<br />
OH<br />
CH 2 S<br />
H 9 C 4<br />
Figure 4.3: 2,14-Dithiacalix[4]arene<br />
C 4 H 9<br />
of replaced phenol with lignin in the resin can be increased by hydrolysis<br />
of the lignin with hydrochloric acid. 23<br />
The modification of PF resins with cornstarch <strong>and</strong> lignin promotes<br />
the condensation reactions. Increased molar masses <strong>and</strong> a high yield of<br />
methylene bridges are found. 24<br />
4.2.7.2 Hydrogen peroxide modifier for particleboards<br />
The addition of H 2 O 2 to a phenolic resin results in greater reactivity of the<br />
phenolic resin <strong>and</strong> increases the mechanical properties of particleboards.<br />
No significant influence of H 2 O 2 on the water resistance of the particleboards<br />
has been observed. 25<br />
4.2.7.3 Calixarenes<br />
Calixarenes are cyclic phenol/formaldehyde oligomers. They have unusual<br />
<strong>and</strong> interesting properties. 2,14-Dithiacalix[4]arene, c.f. Figure 4.3, can be<br />
prepared by acid-catalyzed cyclocondensation of 2,2 ′ -thiobis[4-tert-butylphenol]<br />
with formaldehyde. 26
Phenol/formaldehyde Resins 249<br />
OH<br />
O<br />
O<br />
O<br />
OH -<br />
O<br />
HCHO<br />
O<br />
CH 2<br />
H<br />
OH<br />
O -<br />
CH 2 OH<br />
O<br />
O<br />
O -<br />
HCHO<br />
H<br />
CH 2<br />
OH<br />
CH 2 OH<br />
Figure 4.4: Reaction Mechanism for the Addition of Formaldehyde on Phenol in<br />
Basic Medium 27<br />
4.2.8 Synthesis<br />
4.2.8.1 Mechanism<br />
The basic mechanism of the addition of formaldehyde is shown in Figure<br />
4.4. The catalyst can be a hydroxide anion <strong>and</strong> a metal cation. The hydroxide<br />
anion contributes to the formation of phenates by abstracting the<br />
alcoholic proton.<br />
The rate constants correlate with the radius of the metal cation, as<br />
shown in Table 4.6. The metal hydroxide catalysts can be classified into<br />
two families according to the valency of the cation: KOH, NaOH, <strong>and</strong><br />
LiOH; <strong>and</strong> Ba(OH) 2 <strong>and</strong> Mg(OH) 2 .<br />
4.2.8.2 Kinetic Models<br />
The kinetics of the polymerization of resol has been modelled taking into<br />
account the phenol <strong>and</strong> formaldehyde equilibria. The kinetic parameters
250 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 4.6: Rate Constants, <strong>and</strong> Ionic Radius 27<br />
Cation k[lmol −1 h −1 ] Ionic radius [Å]<br />
K + 0.106 3<br />
Na + 0.119 4<br />
Li + 0.153 6<br />
Ba 2+ 0.164 5<br />
Ca 2+ 0.226 6<br />
Mg 2+ 0.413 8<br />
have been obtained by adjusting the experimental data. The influence of<br />
the type <strong>and</strong> amount of catalyst, the initial pH, the initial molar ratio of<br />
formaldehyde to phenol <strong>and</strong> the condensation temperature on the kinetic<br />
rate constants can be described. 28<br />
4.2.8.3 Preparation<br />
A resol type phenol/formaldehyde resin may be prepared by reacting a molar<br />
excess of formaldehyde with phenol under alkaline reaction conditions.<br />
Formaldehyde is used in an amount between about 0.5 <strong>and</strong> 4.5 mol per mol<br />
of phenol, with the preferred ranges dependent on the application. The free<br />
formaldehyde is typically between 0.1% <strong>and</strong> 15%. The free phenol content<br />
is typically between 0.1% <strong>and</strong> 20%.<br />
Reaction Conditions. Alkaline reaction conditions are established by<br />
adding an alkaline catalyst to an aqueous solution of the phenol <strong>and</strong> formaldehyde<br />
reactants. During the initial reaction of the phenol <strong>and</strong> formaldehyde,<br />
only that amount of alkaline catalyst necessary to produce a resin<br />
need be added to the reaction nature. Typically, an amount of 0.005 to 0.01<br />
mol of alkaline catalyst per mol of phenol is used. Sodium hydroxide is<br />
the most popular catalyst.<br />
Polycondensation of phenol <strong>and</strong> formaldehyde is typically carried<br />
out at a temperature in the range from about 30°C to about 110°C, over a<br />
reaction time of about 1 hour to about 20 hours, using a formaldehyde to<br />
phenol mole ratio in the range from about 1 to about 6. 22<br />
Formaldehyde to Phenol Ratio. A typical phenolic resin to be used as a<br />
binder for fiberglass is made at a formaldehyde/phenol mole ratio as high
Phenol/formaldehyde Resins 251<br />
as 6, to virtually eliminate free phenol in the resin. The high formaldehyde/phenol<br />
ratio required to achieve the very low free phenol concentration<br />
results in free formaldehyde concentrations as high as 20%. The high percentage<br />
of free formaldehyde in the resin must be scavenged by the addition<br />
of a large amount of urea or any other formaldehyde scavengers. 22<br />
4.2.8.4 Structure<br />
A part of a structure of a novolak resin <strong>and</strong> a resol resin is shown in Figure<br />
4.5. A resol prepolymer differs from a novolak resin in that it contains not<br />
only methylene bridges but also reactive methylol groups <strong>and</strong> dimethylene<br />
ether bridges.<br />
13 C-NMR spectroscopy has proven to be the most successful <strong>and</strong><br />
informative analytical tool to analyze resol resins. Using chromium(III)acetylacetonate<br />
as a relaxation agent, quantitative 13 C-NMR spectra can be<br />
obtained. 29<br />
4.2.9 Catalysts<br />
The common catalysts for the phenol/formaldehyde resol synthesis are<br />
shown in Table 4.7. The catalyst type influences the rate of reaction of<br />
phenol <strong>and</strong> formaldehyde <strong>and</strong> the final properties of the resins. 27<br />
The substitution of phenol with formaldehyde in the ortho-position<br />
versus para-position increases in the following sequence of hydroxide catalyst<br />
metals: K < Na < Li < Ba < Sr < Ca < Mg. 30<br />
Among the tetraalkylammonium hydroxides, it is advantageous to<br />
use tetramethyl- or tetraethylammonium hydroxides as catalysts rather than<br />
tetrapropyl- or tetrabutylammonium hydroxides, because the resins prepared<br />
with the last two catalysts have a limited miscibility of the resins<br />
obtained with water. 30<br />
4.2.9.1 Inorganic Catalysts<br />
Phenolic resins are widely used as binders in the fiberglass industry. Most<br />
resins for the fiberglass industry are catalyzed with inorganic catalysts because<br />
of their low cost <strong>and</strong> non-volatility.<br />
When an inorganic base-catalyzed phenolic resin is mixed with urea<br />
solution, a so-called premix or prereact, certain components of the phenolic<br />
resin, such as tetradimers, crystallize out, causing the blockage of lines,
252 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
OH<br />
OH<br />
OH<br />
CH 2<br />
CH 2<br />
CH 2<br />
OH<br />
CH 2<br />
OH<br />
CH 2<br />
Novolak<br />
OH<br />
OH<br />
OH<br />
CH 2<br />
CH 2<br />
CH 2<br />
CH 2<br />
OH<br />
O<br />
CH 2<br />
CH 2<br />
OH<br />
CH 2 OH<br />
Resol<br />
Figure 4.5: Structure of Novolak <strong>and</strong> Resol Resins
Phenol/formaldehyde Resins 253<br />
Table 4.7: Common Catalysts for the Phenol/formaldehyde Resol Synthesis<br />
Catalyst<br />
Reference<br />
Sodium hydroxide, potassium hydroxide, lithium hydroxide<br />
31, 32<br />
Magnesium hydroxide, calcium hydroxide, barium hydroxide<br />
Sodium carbonate<br />
Calcium oxide, magnesium oxides<br />
Tertiary amines, triethylamine<br />
2-Dimethylamino-2-methyl-1-propanol,<br />
32<br />
2-(dimethylamino)-2-(hydroxymethyl)-1,3-propanediol<br />
Tri(p-chloro phenyl)phosphine,<br />
32<br />
triphenylphosphine<br />
Tetraalkylammonium hydroxide<br />
30<br />
interrupting normal operations, <strong>and</strong> the loss of resin. The crystallized material<br />
is difficult to dissolve <strong>and</strong> hinders uniform application of the resin to<br />
the glass fiber.<br />
The tetradimer tends to crystallize in premix solutions of inorganic<br />
base-catalyzed resins <strong>and</strong> urea. Precaution must be taken with the inorganic<br />
base-catalyzed resins to avoid tetradimer crystal growth. For example,<br />
problems can be minimized by regular cleaning of the storage tanks<br />
<strong>and</strong> lines, <strong>and</strong> by shortening the time between the preparation <strong>and</strong> use of<br />
the premix solution. 22<br />
4.2.9.2 Organic Catalysts<br />
Phenolic resins catalyzed with an organic catalyst are especially useful<br />
for applications where high moisture resistance <strong>and</strong> higher mechanical<br />
strength are required. When a phenolic resin such as PF resin catalyzed<br />
with an organic catalyst is mixed with an amino resin such as urea/formaldehyde<br />
(UF) resin, the resultant PF/UF or PF/U is expected to be much<br />
more storage stable <strong>and</strong> to have much less tetradimer precipitation or crystallization.<br />
The organic catalyst, unlike an inorganic base, will increase the solubility<br />
of the phenolic resin in the PF/UF solution. A PF/UF mixture or<br />
premix is often used as a binder in the fiberglass industry. 22<br />
The activation energy of curing of UF resins is generally higher than<br />
that of PF resins, but the curing rates of UF resins are faster than those
254 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
of PF resins. 33 Tertiary amino alcohols have been found to be very effective<br />
catalysts for the polycondensation of phenol <strong>and</strong> formaldehyde, <strong>and</strong><br />
yet they are essentially non-volatile so that attendant amine emissions are<br />
negligible. Because the tertiary amino alcohols are organic catalysts, they<br />
produce resins which are essentially ashless, <strong>and</strong> thus are particularly useful<br />
in the manufacture of resins suitable for use in many industries.<br />
The resulting phenol/formaldehyde resol resin is characterized by<br />
the high moisture resistance <strong>and</strong> high mechanical strength of resins produced<br />
with the use of organic rather than inorganic catalysts. These organic<br />
catalysts also produce phenol/formaldehyde resol resins having superior<br />
tetradimer storage stability, when mixed with a formaldehyde scavenger<br />
such as urea. 22<br />
The tertiary amino alcohol catalyst remains in the resulting reaction<br />
product, <strong>and</strong> at least a portion of the catalyst becomes chemically bound to<br />
the polymeric matrix in the resol resin. The presence of the hydroxyl functionality<br />
on the amino alcohol molecule acts as a plasticizer <strong>and</strong> increases<br />
the flow of the hot resin melt, thereby increasing the resin efficiency <strong>and</strong><br />
yielding a stronger bond of the resin with materials which are integrated<br />
with the resin, such as fiberglass. The chemical bonding of the catalyst to<br />
the polymeric matrix also further inhibits catalyst emissions in the finished<br />
product. 22<br />
4.2.10 Manufacture<br />
4.2.10.1 Exothermic Hazards<br />
The reaction of phenol with formaldehyde is highly exothermic. Therefore,<br />
there is a hazard situation owing to the high released heat in case of<br />
improper operation in industrial scale. From kinetic data, the conditions of<br />
a thermal explosion has been modelled. 34<br />
4.2.10.2 Distillation<br />
When a distillation step is required, the distilled resin can be solvated in<br />
an alcohol, such as methanol, isopropanol, or ethyl alcohol. This is typical<br />
for paper saturating resins. 35 These resins are usually neutralized to a pH<br />
of 6.5 to 7.5 with acid to give lighter color cure.
4.3 SPECIAL ADDITIVES<br />
4.3.1 Low Emission Types<br />
Phenol/formaldehyde Resins 255<br />
It is often desirable to scavenge the free formaldehyde prior to application.<br />
This is done for several reasons:<br />
1. To reduce the extent of human exposure during manufacture,<br />
2. To reduce the free formaldehyde emissions during the forming <strong>and</strong><br />
curing of the insulation product,<br />
3. To reduce the free formaldehyde prior to the addition of an acid<br />
catalyst,<br />
4. To reduce the cost of the binder, <strong>and</strong><br />
5. To improve the anti-punk properties of the resin.<br />
4.3.1.1 Release of Phenol<br />
A problem is the release of volatile organic components, such as phenol,<br />
into the atmosphere during curing. Typical levels of free phenol in a<br />
phenol/formaldehyde resin are in the range of 5 to 15%. One method of<br />
reducing the free phenol level in the base phenol/formaldehyde resin is to<br />
increase the amount of formaldehyde (relative to the phenol) in the resin as<br />
manufactured. Unfortunately this usually results in a more brittle resin that<br />
when cured is unacceptable for manufacturing postforming laminates. 35<br />
4.3.1.2 Urea Scavenger<br />
Often urea cannot be added to the phenolic resin by the manufacturer, because<br />
the mixture of phenolic resin <strong>and</strong> urea, i.e., the premix, is not sufficiently<br />
stable to permit its storage for two to three weeks without tetradimer<br />
precipitation. 22<br />
If urea is added as scavenger to the phenolic resin in a premix system,<br />
it lasts many days before the resin has to be used. During this time,<br />
virtually all the free formaldehyde in the resin reacts with the added urea.<br />
The free formaldehyde content in the premix can then be as low as 0.1%.<br />
The use of such a ready-for-sale premix system reduces the emission of<br />
free monomer. 22
256 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
4.3.1.3 Scavengers for Formaldehyde<br />
The most common scavengers for formaldehyde are chemical species containing<br />
a primary or secondary amine functionality. Examples include urea,<br />
ammonia, melamine, <strong>and</strong> dicy<strong>and</strong>iamide. The most common, <strong>and</strong> the<br />
most economical, amine species is urea. 35<br />
The addition of formaldehyde scavengers to a phenol/formaldehyde<br />
resin requires a finite period of time to achieve equilibrium with the free<br />
formaldehyde in the resin. The process of reaching this equilibrium is<br />
referred to as prereaction, <strong>and</strong> the time to reach the equilibrium is referred<br />
to as the prereact time. Prereact times vary with temperature <strong>and</strong> amine<br />
species. When urea is used, the prereaction times range from 4 to 16 hours,<br />
depending on temperature.<br />
The mole ratio of formaldehyde to formaldehyde scavenger is important,<br />
<strong>and</strong> the conditions must be optimized to achieve the best performance<br />
of the binder resin. With urea, the mole ratio of formaldehyde<br />
to urea is optimally maintained between 0.8 <strong>and</strong> 1.2. At a lower level,<br />
the opacity increases significantly along with the ammonia emissions. At<br />
higher levels the formaldehyde emissions increase <strong>and</strong> the risk of precipitation<br />
of dimethylolurea is greatly increased. That is why in traditional<br />
binders using urea as the formaldehyde scavenger, the extension level is<br />
dictated by the amount of free formaldehyde in the base resin.<br />
However, disadvantages arise when the resins are prereacted with<br />
urea prior to forming the binder. Because free formaldehyde stabilizes the<br />
tetradimer in the resin, prereacting with urea will reduce the amount of free<br />
formaldehyde in the resin, hence reducing the shelf life of the formulation.<br />
In addition, prereacting with urea takes time, requires prereact tanks <strong>and</strong><br />
binder tanks, <strong>and</strong> urea needs to be stored in heated storage tanks.<br />
4.3.1.4 Over-condensing<br />
The reduction of residual free formaldehyde can be achieved by over-condensing<br />
the resin. 36 An over-condensed resol denotes a resin in which a<br />
relatively high proportion of large oligomers is formed at the end of the<br />
condensation stage. It has a high average molecular weight, higher than<br />
500 Dalton. Such a resol is obtained by increasing the reaction time or the<br />
reaction temperature to ensure a virtually quantitative conversion of the<br />
initial phenol while going beyond the monocondensation to monomethylolphenols.<br />
It contains a very low proportion of free phenol <strong>and</strong> volatile
Phenol/formaldehyde Resins 257<br />
phenolic compounds capable of polluting the atmosphere at the site of use.<br />
4.3.1.5 Aqueous Dispersions of Phenol/formaldehyde Resins<br />
Aqueous dispersions of phenol/formaldehyde resol resins are frequently<br />
used in the manufacture of mineral fiber insulation materials, such as insulating<br />
glass fiber batts for walls, in roofs <strong>and</strong> ceilings, <strong>and</strong> insulating<br />
coverings for pipes.<br />
Typically, after the glass fiber has been formed, the still hot fiber<br />
is sprayed with aqueous binder dispersion in a forming chamber or hood,<br />
with the fibers being collected on a conveyer belt in the form of a wool-like<br />
mass associated with the binder. In some cases, a glass fiber web is sprayed<br />
with the aqueous dispersion.<br />
Both resol <strong>and</strong> urea-modified resol resins have been employed for<br />
this purpose. The urea contributes to the punking resistance of the binder<br />
(i.e., resistance to exothermic decomposition at elevated temperatures), <strong>and</strong><br />
reduces volatile compounds when the resin is cured at elevated temperatures.<br />
37 To improve the performance of the binder for glass fibers, a lubricant<br />
composition, such as a mineral oil emulsion, <strong>and</strong> a material promoting the<br />
adhesion of the resol resin to the glass fibers, such as a suitable silane, can<br />
be added. An example of an adhesion-improving silane is (3-aminopropyl)triethoxysilane.<br />
37<br />
4.3.2 Boric Acid-modified Types<br />
Boric acid-modified phenolic resins (BPFR) show excellent performance,<br />
such as thermal stability, mechanical strength, electric properties <strong>and</strong> further<br />
shielding of neutron radiation. 38<br />
Because bisphenol F has a methylene group, it shows a higher freedom<br />
of rotation in contrast to bisphenol A-based materials. The reaction<br />
of bisphenol F, formaldehyde <strong>and</strong> then with boric acid is shown in Figure<br />
4.6. At elevated temperatures the boric acid forms a six-membered ring<br />
structure containing a boron oxygen coordination bond. 39 The curing reaction<br />
of BPFR follows an autocatalytic kinetics mechanism. 40 The cured<br />
structure of BPFR formed from the paraformaldehyde method is different<br />
from BPFR formed from the formalin method. The structure in this curing<br />
BPFR does not contain ether bonds <strong>and</strong> carbonyl groups. The thermal<br />
stability of this BPFR is better than BPFR formed from formalin. 41
258 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
HO<br />
CH 2<br />
OH<br />
CH 2 O<br />
HO<br />
CH2<br />
CH 2<br />
OH<br />
HO<br />
CH 2<br />
OH<br />
H 3 BO 3<br />
HO<br />
CH 2<br />
OH<br />
HO<br />
CH 2<br />
CH 2<br />
O<br />
B<br />
OH<br />
HO<br />
CH 2<br />
CH 2<br />
O<br />
HO<br />
CH 2<br />
OH<br />
H 2 C<br />
CH 2 O O CH 2<br />
B<br />
O O<br />
H<br />
CH 2<br />
Figure 4.6: Reaction of Bisphenol F with Formaldehyde <strong>and</strong> Boric Acid
Phenol/formaldehyde Resins 259<br />
CH 2<br />
R<br />
O<br />
CH 2<br />
R<br />
Figure 4.7: Formation of Xanthens 42<br />
The weight loss for a common bisphenol F resin is more than 99%<br />
at 580°C, while the boron-modified resin shows only 45% at 700°C. The<br />
situation is completely similar for a bisphenol A resin. 38<br />
4.3.3 Fillers<br />
Many fillers are known for PF resins, such as glass fibers, ceramic material,<br />
<strong>and</strong> organic fiber materials.<br />
4.3.3.1 Jute Reinforcement<br />
Jute textile can be recycled into composites using 12 to 30% of phenol/-<br />
formaldehyde (PF) resin. The dimensional stability of the produced composites<br />
can be improved by acetylating or by steam treatment of the jute<br />
textile. Steaming the jute textile is superior to acetylation in improving the<br />
dimensional stability. A steamed jute textile exhibits much less irreversible<br />
<strong>and</strong> reversible swelling than acetylated or untreated jute textile. 43<br />
4.3.4 Flame Retardants<br />
4.3.4.1 Pyrolysis products<br />
The main products of pyrolysis of both novolaks <strong>and</strong> resols are phenol,<br />
2-methylphenol, 4-methylphenol, 2,4,6-trimethylphenol, <strong>and</strong> xanthens. 42<br />
Xanthens arise because of cyclization reactions, as shown in Figure 4.7.
260 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
OH<br />
OH<br />
H 3 C CH 2<br />
O<br />
H 2 C CH 3<br />
OH<br />
OH<br />
H 3 C CH 2<br />
CH 3<br />
CH 3<br />
OH<br />
OH<br />
CH 3<br />
H 3 C<br />
H 2 C<br />
CH 3<br />
CH 3<br />
CH 3<br />
Figure 4.8: Self-condensation of 2-Hydroxymethyl-4,6-dimethylphenol<br />
4.3.4.2 Brominated Phenol/formaldehyde Resin<br />
A brominated phenol/formaldehyde resin with ca. 10% bromine has been<br />
shown to be a good plywood adhesive that shows a high shear strength,<br />
good flame retardancy, <strong>and</strong> good resistance to both hot <strong>and</strong> cold water. 44<br />
4.4 CURING<br />
4.4.1 Model Studies<br />
The mechanism of curing has been investigated using model compounds.<br />
2-Hydroxymethyl-4,6-dimethylphenol condenses at 120°C into bis(2-hydroxy-3,5-dimethylbenzyl)ether<br />
<strong>and</strong> bis(2-hydroxy-3,5-dimethyl-benzyl)-<br />
methylene as shown in Figure 4.8. The ether is formed much faster than<br />
the methylene compound. Phenol does not act as an acid catalyst for ether<br />
hydrolysis.<br />
Previous results suggest that during curing at temperatures above<br />
150°C, quinone methides have been proposed as key intermediates. However,<br />
at temperatures below 150°C, quinone methides have not been considered<br />
as important, which has been contradicted. 45 Figure 4.9 illustrates<br />
the formation of quinone methides. Quinone methides can be formed by<br />
the intramolecular dehydration of 2-hydroxymethyl-4,6-dimethylphenol.<br />
Further, they can be formed by a retro Diels-Alder reaction of a trimer.<br />
With phenol <strong>and</strong> 2-methylphenol, a quinone methide attacks exclusively
Phenol/formaldehyde Resins 261<br />
OH<br />
OH<br />
O<br />
H 3 C CH 2<br />
-H 2 O<br />
H 3 C CH 2<br />
CH 3<br />
CH 3<br />
O<br />
OH<br />
OH<br />
OH<br />
H 3 C CH 2<br />
H 3 C CH 2<br />
CH 3<br />
CH 3<br />
Figure 4.9: Formation <strong>and</strong> Reaction of Quinone Methides<br />
the free ortho site of the phenol. Therefore, a high ortho bridged resin<br />
should be formed under conditions that favor the formation of an ortho<br />
quinone methide. This would require a resin which contains predominately<br />
ortho hydroxymethyl substituents, <strong>and</strong> condensation at high temperature,<br />
preferably in solvents which encourage the dehydration of the ortho hydroxymethyl<br />
functionality. 45 Phenoxy bridges are shown to be formed by<br />
ether exchange between phenolic OH <strong>and</strong> a bridging ether.<br />
Evaluation of nonisothermal DSC curing data by isoconversional<br />
analysis revealed that the activation energy changes with conversion in the<br />
course of curing. The data were interpreted to show that the curing process<br />
of phenol/formaldhyde resins undergoes a change in the reaction mechanism<br />
from a kinetic to a diffusion regime. 46<br />
4.4.2 Experimental Design<br />
Factorial experiments have been conducted to find the effect of the monomer<br />
feed on the structure of resol resins.<br />
47, 48<br />
The amount of ortho <strong>and</strong><br />
para methylol phenols increases with the F/P ratio. An increased condensation<br />
viscosity also increases the weight-average molecular weight.<br />
Among the parameters investigated, the viscosity has the strongest effect<br />
on the molecular weight. Several other useful relations could be established<br />
by the statistical approach.
262 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
4.4.3 Water Content<br />
The amount of water in a powder resol resin was shown to play an important<br />
part in the curing kinetics. In the initial curing stages, water acts as a<br />
diluent <strong>and</strong> retards the curing. At the higher conversions, water acts as a<br />
plasticizer <strong>and</strong> contributes to enhancing the final conversion. 49<br />
4.4.4 Influence of Pressure<br />
Curing under high-pressure conditions reveals competition between the<br />
oxidation <strong>and</strong> polymerization reactions. This results in fewer methylene<br />
bridges <strong>and</strong> more free ortho-positions. Thus, a consequent lower degree of<br />
polymerization is reached. 50<br />
4.4.5 Wood<br />
The activation energy of the curing reaction of a PF resin generally increases<br />
when PF resin is mixed with wood. This is caused mainly by the<br />
decrease of the pH resulting from the presence of wood. 51 Further, wood<br />
decreases the curing enthalpy. This effect can be interpreted in that the<br />
final conversions are lowered.<br />
4.4.6 Novolak Curing Agents<br />
Several curing agents for novolak resins are known in the art, including<br />
formaldehyde, paraformaldehyde, <strong>and</strong> hexamethylenetetramine. The most<br />
common curing agent is hexamethylenetetramine, which reacts upon heating<br />
to yield ammonia <strong>and</strong> cured resin. These curing agents complete the<br />
crosslinking reaction to convert a thermoplastic novolak resin to an insoluble<br />
infusible state. 4<br />
4.4.6.1 Hexamethylenetetramine<br />
When hexamethylenetetramine is used, ammonia evolves during curing of<br />
the novolak resin. In addition, novolak curing agents like hexamethylenetetramine<br />
typically require curing temperatures as high as 150°C. The cure<br />
temperatures can be lowered by the addition of acids, but this often introduces<br />
other problems such as die staining, die sticking, <strong>and</strong> sublimation of<br />
organic acids into the atmosphere.
Phenol/formaldehyde Resins 263<br />
4.4.6.2 Triazine-type Hardeners<br />
Hardeners of the triazine-type are alkoxylated melamine/formaldehyde resins<br />
or alkoxylated benzoguanamine-formaldehyde resins.<br />
These hardeners have a water solubility of less than 15% by weight<br />
<strong>and</strong> contain from 1 to 2.5 melamine or benzoguanamine rings per molecule.<br />
About 7% to 15% of triazine hardener is used.<br />
The triazine hardeners are prepared from melamine or benzoguanamine<br />
<strong>and</strong> formaldehyde with at least 4 mol formaldehyde per mol melamine<br />
or benzoguanamine to produce melamine/formaldehyde resins or<br />
benzoguanamine-formaldehyde resins, e.g., hexakis(methylol)melamine in<br />
the case of a melamine/formaldehyde resin. These formaldehyde resins are<br />
subsequently alkoxylated with, e.g., butoxymethyl groups. 52<br />
Melamine resins typically require either an acid catalyst or elevated<br />
temperatures to cure a novolak resin. Melamine resin curing agents<br />
also tend to cure novolak resins more slowly than hexamethylenetetramine.<br />
They produce a lesser extent of cure, <strong>and</strong> frequently produce formaldehyde<br />
in a side reaction. 4<br />
4.4.6.3 Substituted Melamines<br />
The most common methylene donor for crosslinking novolak resins is<br />
hexamethylenetetramine (HMTA), but it has the following drawbacks:<br />
• It raises problems of health <strong>and</strong> safety.<br />
• When novolak resins are used with HMTA in the presence of rubbers<br />
intended to adhere to metal reinforcements, this bond may<br />
take deteriorate.<br />
HMTA as hardener can be replaced by another methylene donor,<br />
hexa(methoxymethyl)melamine (H3M). 8 This can be used in conjunction<br />
with a urea, amide, or imide, such as propionamide. This compound liberates<br />
methanol instead of ammonia in the course of curing. 8<br />
4.4.7 Resol Resin Hardeners<br />
Resol resins have also been used as a curing agent for novolak resins. 53<br />
A comparatively large amount of resol is required to achieve a reasonable<br />
crosslink density.
264 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
A disadvantage is that resol resins have a limited shelf life, caused<br />
by self-condensation wherein the phenolic nuclei are bridged by methylene<br />
groups. Resol resins may contain significant levels of free phenol<br />
<strong>and</strong> formaldehyde that may present environmental concerns. Conventional<br />
resol resins typically contain 4 to 6% free phenol <strong>and</strong> may contain approximately<br />
1% free formaldehyde. 4<br />
4.4.7.1 Benzoxazine Curing Agent<br />
An alternative curing agent for a novolak resin is a benzoxazine polymer. 54<br />
Benzoxazine may be an intermediate product in the reaction of hexamethylenetetramine<br />
(HMTA) <strong>and</strong> phenol or substituted phenols. Benzoxazine<br />
is the Mannich product of a phenolic compound, an aldehyde <strong>and</strong> a primary<br />
amine. A benzoxazine polymer composition may be manufactured<br />
by combining an alcoholate of an amino triazine such as melamine, guanamine,<br />
benzene guanamine, an aldehyde <strong>and</strong> a resol, <strong>and</strong> allowing these<br />
to react under conditions favorable to benzoxazine formation.<br />
4.4.8 Ester-type Accelerators<br />
Certain esters can accelerate the curing of PF resins, for example, ethyl<br />
formate, propylene carbonate, γ-butyrolactone, <strong>and</strong> triacetin. 55 A mechanism<br />
for the action of these accelerators has been proposed. The first step<br />
consists of transesterification with the methylol group of the resin. Then,<br />
the ester group is attacked by another aromatic compound in the ortho or<br />
para position, or it is converted to a reactive quinone methide intermediate,<br />
which reacts by the quinone methide mechanism.<br />
4.4.9 Ashless Resol Resins<br />
Ashless resins are prepared from organic ingredients; no inorganic catalyst<br />
should be used. The catalysts commonly used in phenolic resin production<br />
are sodium hydroxide <strong>and</strong> triethylamine (TEA). TEA is very volatile<br />
<strong>and</strong> toxic. Its emission into the atmosphere is regulated by government<br />
agencies.<br />
Ashless <strong>and</strong> low-ash phenolic resol resins having no amine odor can<br />
be prepared by reacting phenol <strong>and</strong> formaldehyde in the presence of a low<br />
volatile <strong>and</strong> strongly basic tertiary amino alcohol, such as 2-dimethylamino-2-methyl-1-propanol<br />
(DMTA) or 2-(dimethylamino)-2-(hydroxymeth-
Amine<br />
Phenol/formaldehyde Resins 265<br />
Table 4.8: Basicity of Amines <strong>and</strong> Aminoalcohols<br />
pH a<br />
Triethylamine 10.8<br />
2-Dimethylamino-2-methyl-1-propanol 10.7<br />
2-(Dimethylamino)-2-(hydroxymethyl)-1,3-propanediol (80%) 10.6<br />
a 0.010 N aqueous solution<br />
yl)-1,3-propanediol (DMAMP). 22 These tertiary amino alcohols have a<br />
boiling point above 250°C. A comparison of the pH of 0.010 N solutions<br />
of these amino alcohols along with that of triethylamine is shown in Table<br />
4.8, indicating that DMTA <strong>and</strong> DMAMP (80%) are as basic as TEA. 22<br />
4.4.10 Recycling<br />
4.4.10.1 Porous Fiberboard from Waste Newspapers<br />
Flame retardant <strong>and</strong> waterproof porous fiberboards can be manufactured<br />
from waste newspapers by using a foaming agent <strong>and</strong> a reinforcing phenol/formaldehyde<br />
resin. 56 A water-soluble phenol/formaldehyde resin of the<br />
resol type is used in amounts of 11% to obtain best quality product. To<br />
increase the porosity, a foaming agent is admixed.<br />
4.4.10.2 Sewage Treatment Process<br />
Modified wastes from phenol/formaldehyde resins <strong>and</strong> exp<strong>and</strong>ed poly(styrene)<br />
can be used in sewage treatment processes. 57 Amino derivatives of<br />
novolak wastes <strong>and</strong> sulfonated derivatives of novolak <strong>and</strong> exp<strong>and</strong>ed polystyrene<br />
wastes are synthesized. These compounds are basically anionic<br />
polyelectrolytes, <strong>and</strong> they exhibit good flocculation properties in purification<br />
processes of a sewage waters of coal-mines, or steel plants. The purification<br />
is effected in that the impurities in the waste water interact with<br />
the polymeric material thus forming insoluble particles. The main mechanisms<br />
of destabilization of the polymeric electrolyte are bridging of the<br />
individual molecules by the impurity mosaic flocculation, <strong>and</strong> charge neutralization.<br />
In mosaic flocculation, the polyelectrolyte adsorbs locally onto<br />
the impurity, so that opposite charged regions may be formed. 58
266 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Use<br />
Table 4.9: Uses for Phenol/formaldehyde Resins 35<br />
Insulation<br />
Plywood <strong>and</strong> engineered lumber<br />
Oriented str<strong>and</strong> board<br />
High pressure laminating resins<br />
Paper saturating resins<br />
Open or closed cell foams<br />
Abrasive binders<br />
Friction binders<br />
Coated foundry s<strong>and</strong> binders<br />
Remarks<br />
Coating fibers<br />
Wafer board resins<br />
Use for flat surfaces<br />
Oil filter, overlay, paint roller tubes<br />
Floral foam supports<br />
4.5 APPLICATIONS AND USES<br />
Phenol/formaldehyde resins are used to make a variety of products including<br />
consolidated wood products such as plywood, engineered lumber,<br />
hard board, fiberboard, <strong>and</strong> oriented str<strong>and</strong> board. Other products include<br />
fiberglass insulation, laminates, abrasive coatings, friction binders, foams,<br />
foundry binders, <strong>and</strong> petroleum recovery binders. They are also used as<br />
paper saturating resins for oil filters, overlay, paint roller tubes, etc. 35 Uses<br />
of phenol/formaldehyde resins are summarized in Table 4.9.<br />
Phenol/formaldehyde foam resins are used to make open or closed<br />
cell foams when cured. Such foams are primarily used to make floral foam<br />
supports for retaining flower stems in water. The foam is able to soak<br />
up water many times its original weight to provide water for the flowers.<br />
These foams are primarily open cell (with openings in cell walls).<br />
Other uses for phenol/formaldehyde foams are dense foams used<br />
for models (similar to balsa wood), to hold jewelry, <strong>and</strong> to make molds<br />
for foot prosthetics. Closed cell foams find use in barrier <strong>and</strong> insulation<br />
applications.<br />
Further uses of phenol/formaldehyde resins include abrasive binders,<br />
friction binders, <strong>and</strong> phenol/formaldehyde coated foundry s<strong>and</strong> binders.<br />
4.5.1 Binders for Glass Fibers<br />
Glass fibers are generally mass produced in two types:<br />
1. Bulk or blown fiber for insulation <strong>and</strong> allied applications,<br />
2. Continuous-filament, or reinforcing fibers.
Phenol/formaldehyde Resins 267<br />
In either form, the raw fiberglass is abrasive <strong>and</strong> fragile. Damage to<br />
the individual glass fibers can occur as a result of the self-abrasive motion<br />
of one fiber passing over or interacting with another fiber. The resulting<br />
surface defects cause reduction in the overall mechanical strength of the<br />
fiberglass.<br />
Consequently, binders have been developed to prevent these problems.<br />
A typical binder may prevent the destructive effects of self-abrasion<br />
without inhibiting the overall flexibility of the finished glass fiber product.<br />
Good resistance <strong>and</strong> resilience to extreme conditions of elevated humidity<br />
<strong>and</strong> temperature are beneficial in view of the wide variety of applications<br />
of glass fiber/binder compositions.<br />
The amount of binder present in a fiberglass product is dependent on<br />
several factors including the product shape, the type of service required,<br />
compressive strength requirements, <strong>and</strong> anticipated environmental variables<br />
such as temperature. 59<br />
4.5.1.1 Phenolic Binders<br />
Traditionally, the performance parameters required for insulation fibers<br />
have been satisfied only with phenol/formaldehyde resins.<br />
Therefore, glass fiber binders have been almost exclusively based on<br />
phenol/formaldehyde resins. These systems typically include aminoplast<br />
resins such as melamine <strong>and</strong> urea, silicone compounds, soluble or emulsified<br />
oils, wetting agents, <strong>and</strong> extenders or stabilizers.<br />
Typically phenolic binders contain large amounts of low molecular<br />
weight species including phenol, formaldehyde, <strong>and</strong> volatile phenol/formaldehyde<br />
adducts such as 2-methylolphenol <strong>and</strong> 4-methylolphenol.<br />
During the curing process, these volatile low molecular weight components<br />
are released into the atmosphere in substantial volumes as volatile<br />
organic compounds (VOCs).<br />
Since the process of manufacturing fiberglass typically involves spraying<br />
large volumes of phenol/formaldehyde binders into high volume air<br />
streams, <strong>and</strong> then curing the product in convection ovens that involve high<br />
volumes of air, fiberglass manufacturers have an urgent need to reduce their<br />
VOC emissions, particularly with regard to formaldehyde. 59<br />
Reducing the free formaldehyde content of typical phenol/formaldehyde<br />
binders affects the final product quality, because an excess of formaldehyde<br />
is essential for curing <strong>and</strong> bonding in such systems. Attempts
268 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
to convert free formaldehyde into less obnoxious <strong>and</strong> dangerous chemicals<br />
have involved the addition of ammonia or urea. Such additions were<br />
intended to convert free formaldehyde into hexamethylenetetramine or a<br />
mixture of mono <strong>and</strong> dimethylol ureas.<br />
Unfortunately, urea, hexamethylenetetramine, <strong>and</strong> mono <strong>and</strong> dimethylol<br />
ureas can all contribute to the production of trimethylamine, which<br />
gives the cured phenolic binder <strong>and</strong> finished product an undesirable fishy<br />
odor. In addition, nitrogen-containing compounds can decompose to yield<br />
ammonia <strong>and</strong> other potentially harmful volatile compounds. Phenol/formaldehyde<br />
resins require careful h<strong>and</strong>ling procedures. Since the cooked resin<br />
must be refrigerated until use, refrigerated trucks <strong>and</strong> holding tanks are<br />
required. Even with refrigeration, the storage time of a phenolic resin is<br />
typically 15 days.<br />
4.5.2 Molding<br />
In the plastics molding field, phenolic resins have been a preferred choice<br />
as molding material for precision parts that must function in hostile environments.<br />
Phenolic resins form crosslinked structures with excellent dimensional,<br />
chemical, <strong>and</strong> thermal stability at elevated temperature.<br />
4.5.3 Novolak Photoresists<br />
A positive photoresist composition can comprise a 1,2-naphthoquinonediazide<br />
compound <strong>and</strong> a novolak resin. The composition is sensitive to<br />
ultraviolet rays.<br />
7, 60<br />
The photosensitizer is mainly a naphthoquinonediazidesulfonic acid<br />
ester. The content of the photosensitizer is 20 to 60 parts per 100 parts<br />
by weight of the substituted phenol novolak resin. Suitable phenols for<br />
this special application are mixtures of 2-cyclohexyl-5-methylphenol, m-<br />
cresol, <strong>and</strong> p-cresol. The phenols are condensed with formaldehyde. Suitable<br />
solvents include methylisobutylketone or 2-heptanone. 7<br />
The unexposed photoresist is not soluble in alkaline medium. The<br />
insolubility is attributed due to an azo coupling of the sensitizer with the<br />
novolak polymer. Exposure to UV-light converts the o-diazonaphthoquinone<br />
into an indene carboxylic acid, c.f. Figure 4.10. The carboxylic groups<br />
enhance the solubility of the lacquer, so that the material becomes soluble<br />
in an alkaline medium.
Phenol/formaldehyde Resins 269<br />
O<br />
N + N -<br />
hν<br />
O<br />
C<br />
SO 3 H<br />
H 2 O<br />
SO 3 H<br />
O<br />
C OH<br />
SO 3 H<br />
Figure 4.10: Conversion of o-Diazonaphthoquinone by Radiation<br />
4.5.4 High Temperature Adhesives<br />
Resol melamine dispersions in which melamine is solubilized are used as<br />
high temperature adhesives, e.g., for glass fibers. The resin has low formaldehyde<br />
content <strong>and</strong> a high alkali ratio. The uncured resins compositions<br />
show improved water solubility. 61<br />
4.5.5 Urethane-modified Types<br />
Cured phenol/formaldehyde resins show considerable fragility <strong>and</strong> a low<br />
impact resistance. The hydroxymethyl groups present enable a chemical<br />
modification with urethane oligomers with isocyanate end groups.<br />
The addition of polyurethane improves the elasticity of the compositions<br />
<strong>and</strong> introduces coupling sites that increase the adhesion properties. 62<br />
In order to decrease the reactivity of the PF resin with oligomer isocyanate<br />
groups <strong>and</strong> to exp<strong>and</strong> the shelf life of such compositions, the methylol<br />
groups can be etherified with butanol. The etherification with butanol<br />
proceeds in the presence of phosphoric acid.
270 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
4.5.6 Carbon Products<br />
Phenol/formaldehyde polymers are increasingly used as precursors for the<br />
production of carbon replacing ceramic <strong>and</strong> pitch-based materials in refractory<br />
applications.<br />
4.5.6.1 Mechanism of Carbonization<br />
The pore sizes of carbons obtained from phenol/formaldehyde resins depend<br />
strongly on the ratio of formaldehyde to phenol (FP) in the initial formulation.<br />
Higher formaldehyde-to-phenol ratios result in higher surface<br />
areas when measured with nitrogen, but similar surface areas measured<br />
with carbon dioxide. 63 This leads to the conclusion that the microporous<br />
structure of the carbon powder is extremely narrow. A comparison of a resin<br />
with a molar ratio of phenol to formaldehyde (F/P) F/P=1.2 <strong>and</strong> F/P=1.8<br />
showed that the differences between the cured resins persisted after heating<br />
to 400°C, when methylene bridge degradation becomes significant. However,<br />
no substantial differences are observable after heating to 500°C.<br />
4.5.6.2 Carbon Membranes<br />
Carbon membranes have gained great interest because of their thermal <strong>and</strong><br />
chemical stability. Carbon membranes are classified according to pore size<br />
as microfiltration membranes. The mean pore diameter ranges from 0.02 to<br />
10 µm, usually from 0.1 to 1 µm. Ultrafiltration membranes have a mean<br />
pore diameter from 1 to 100 nm: gas separation membranes have a mean<br />
pore diameter of less than 1 nm.<br />
Activated carbons can be prepared by controlled pyrolysis of either<br />
natural products, such as coconut shell at 800°C, coal at 400 to 600°C,<br />
wood at 300 to 500°C, or polymeric materials, such as phenol/formaldehyde<br />
resins at 900°C, poly(furfuryl alcohol) at 600°C, or polyimide at 550<br />
to 800°C. 64<br />
Carbon molecular sieve membranes for the separation of hydrogen<br />
- nitrogen <strong>and</strong> hydrogen - methane mixtures have been prepared from a<br />
novolak phenol/formaldehyde resin. The liquid resin is used to form a film<br />
on a porous substrate by dip-coating. A carbon molecular sieve membrane<br />
is then obtained by carbonization of the film.<br />
The pore structure of the carbon membranes can be closely controlled<br />
by adjusting the degree of curing of the raw material. The final pore
Phenol/formaldehyde Resins 271<br />
diameter increases with the amount of hexamethylenetetramine used for<br />
curing.<br />
65, 66<br />
Porous carbon membranes can also be formed on a macroporous<br />
clay support. The process consists of carbonizing a solvent-containing<br />
non-interpenetrating crosslinked resol-type phenol/formaldehyde (PF) resin<br />
film on a macroporous clay substrate. The porous structure of the membrane<br />
seems to result from the evaporation of solvent at the film-making<br />
stage, along with in-situ crosslinking <strong>and</strong> carbonization. 64<br />
4.5.6.3 Porous Carbon Beads<br />
Porous carbon beads can be prepared by carbonization at 1000°C of phenol/formaldehyde<br />
beads under nitrogen or carbon dioxide atmosphere, followed<br />
by oxidation with boiling nitric acid. 67 The carbonization atmospheres<br />
have a remarkable influence on the porosity development <strong>and</strong> structural<br />
changes of the resulting carbon spheres. In comparison with a N 2<br />
atmosphere, a CO 2 atmosphere yields more surface pits, a higher surface<br />
area, <strong>and</strong> a higher micropore volume of the carbon spheres.<br />
4.5.6.4 Carbon Urea Impregnation<br />
Carbons from phenol/formaldehyde resins, which are glass-like, contain a<br />
high proportion of closed pores that are not accessible to gas molecules.<br />
Opening of these closed pores contributes to an increase in the porosity.<br />
Urea, which decomposes at 130 to 400°C, can be employed as an additive<br />
to the resin precursor. The escape of the degradation gases produced by<br />
the impregnated urea during resin carbonization promotes the formation of<br />
micropores in the resulting char.<br />
Carbons of ca. 2000 m 2 /g can be obtained at 70% burn-off by 10%<br />
urea impregnation in the resin, while at a similar burn-off level, carbons<br />
obtained from pure resin can have a surface area around 1400 m 2 /g. 68 The<br />
burn-off level is the weight loss in % of the maximum weight loss.<br />
4.5.6.5 Nitrogen-containing Carbon Catalysts<br />
Activated carbons, because of their high accessible surface area, are used as<br />
supports for certain catalysts. Often, the presence on the surface of heteroelements,<br />
such as oxygen, nitrogen, <strong>and</strong> sulfur, stabilizes loaded metallic<br />
catalysts. Surface oxygen or surface nitrogen can effectively catalyze the
272 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
reduction of NO with NH 3 at low temperatures, compared to metal oxide<br />
catalysts.<br />
Carbon catalyst supports containing nitrogen can be prepared using<br />
implantation of nitrogen by treatment with NH 3 or HCN of a carbon that<br />
has been previously oxidized. Another method consists of the use of nitrogen-containing<br />
polymers. For example, active carbons containing up to<br />
4.5% nitrogen can be prepared by carbonization in argon <strong>and</strong> steam activation<br />
of a vinylpyridine resin. 69<br />
Activated carbon catalysts can be produced from the phenol/formaldehyde<br />
resins that are prepared using ammonia. After synthesis, m-phenylene<br />
diamine (MPDA) dissolved in alcohol is added to the resin as an<br />
additional nitrogen source. Up to 30% of m-phenylene diamine is required<br />
by the process.<br />
The resin can be carbonized using a gasification method. This method<br />
consists of carbonization of the resin in N 2 by heating at 10°C/min from<br />
room temperature to 800°C, followed by gasifying the resulting carbon in<br />
oxygen at 400°C. 70 The main difference between pyrolysis <strong>and</strong> gasification<br />
as used here, is that pyrolysis is conducted in inert atmosphere, but<br />
gasification is a combined thermal treatment in inert gas, ie., N 2 <strong>and</strong> an<br />
oxidizing gas, i.e. O 2 . Ultimate analysis shows that up to 10% of nitrogen<br />
can be incorporated in the carbon char.<br />
4.6 SPECIAL FORMULATIONS<br />
4.6.1 Chemical Resistant Types<br />
Alkaline resistance can be improved by etherification of the phenolic hydroxyl<br />
group. Not more than one third of the phenolic hydroxyl group<br />
should be etherified, otherwise the reactivity would decrease too much.<br />
4.6.2 Ion Exchange Resins<br />
Commercially available ion exchange resins are produced from polymers<br />
such as phenol/formaldehyde, styrene-divinylbenzene, acrylonitrile, acrylates,<br />
<strong>and</strong> polyamines. 71<br />
These polymers can be modified by halomethylation, sulfonation,<br />
phosphorylation, carboxylation, etc. This additional reaction enables the<br />
production of an ion exchange resin with specific reactive sites, thereby<br />
exhibiting greater selectively towards particular metal ions or other anions
Phenol/formaldehyde Resins 273<br />
or cations. In conventional practice, the ion exchange resins are produced<br />
in bead or granular form, the bead size generally varying from 40 µm to<br />
greater than 1 mm in diameter. A particular advantage of phenolic resins<br />
is that they are chemically resistent.<br />
4.6.3 Brakes<br />
Phenolic-bonded composites for Industrial brake applications often contain<br />
partially dehydrated vermiculite particles to generate friction. Dehydration<br />
<strong>and</strong> rehydration processes of vermiculite should take place. The maximum<br />
detected temperature on the friction surface of certain investigated composite<br />
samples after friction test was 900°C. 72<br />
4.6.4 Waterborne Types<br />
Generally waterborne laminating resins are similar to the solvent-borne<br />
types except they lack an organic solvent <strong>and</strong> have usually lower molecular<br />
weight than their solvent-borne counterparts. Because they have lower<br />
molecular weight, they typically have a higher level of free phenol.<br />
4.6.5 High Viscosity Novolak<br />
High molecular weight, thermoplastic phenol/formaldehyde is a suitable<br />
compatibilizer for poly(propylene)-phenol/formaldehyde resins. The materials<br />
can be blended by reactive extrusion.<br />
A phenol/formaldehyde resin with high molecular weight is required<br />
in reactive extrusion to obtain a favorable viscosity ratio. A mixture of<br />
phenol <strong>and</strong> cresols, tert-butylphenols, <strong>and</strong> resorcinol is used as phenol<br />
component. The resins are highly linear with a molecular weight in the<br />
range of 10 to 30 kDalton. 73<br />
4.6.6 Foams<br />
In order to foam the resin, surfactants or wetting agents are mixed into the<br />
resin to create bubbles. Then a low boiling liquid such as CFC, HCFC,<br />
pentane or hexane is added to the mixture. A strong acid is added to the<br />
resin to initiate curing of the phenol/formaldehyde resin. This reaction<br />
generates heat causing the low boiling liquid to vaporize within the bubbles<br />
in the resin. Consequently a foam is created from this mixture. Typically,
274 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
within 10 minutes the foam rises to its maximum height <strong>and</strong> hardens when<br />
fully cured.<br />
4.6.7 Visbreaking of Petroleum<br />
Mild thermal cracking (visbreaking) of the gas oil fraction boiling above<br />
350°C can be achieved in the presence of 0.5% of a polymeric phenol/-<br />
formaldehyde sulfonate (PFS) used as a promoter. The addition of PFS as<br />
a promoter accelerates the free radical chain reaction. 23<br />
4.7 TESTING METHODS<br />
Several test methods are commonly used to characterize a phenolic resin. 22<br />
Subsequently,these methods are described.<br />
4.7.1 Water Tolerance<br />
Distilled water at 25°C is gradually added to 10 g resin until the resin<br />
solution turns hazy. The water tolerance of a resin is an indication of the<br />
miscibility of the resin with water. It is an important parameter for resin<br />
used in fiberglass binders since the phenolic resin is normally diluted with<br />
water to a concentration as low as 2%. Maintaining a clear solution without<br />
phase separation at such dilution is essential for trouble-free processing <strong>and</strong><br />
for high quality film properties. Typically a water tolerance of 25 times is<br />
required. The higher the water tolerance of the resin is, the lower is the<br />
molecular weight of the resin. A low molecular weight resin has more<br />
polar end groups than a more condensed resin.<br />
4.7.2 Salt Tolerance<br />
For the salt tolerance test, a 10% sodium chloride solution is added to the<br />
phenolic resin solution gradually until the resin solution turns hazy.<br />
This is another method to measure the ability of the resin to mix with<br />
water <strong>and</strong> remain clear without precipitation, similar to water tolerance<br />
except that it is more challenging to the resin.
Phenol/formaldehyde Resins 275<br />
4.7.3 Free Phenol Content<br />
The free phenol content is measured by gas chromatography. It is the<br />
amount of phenol in the resin at the end of synthesis. A lower number<br />
is preferred for increased resin efficiency <strong>and</strong> lower emissions.<br />
4.7.4 Free Formaldehyde<br />
The free formaldehyde content is measured commonly by the hydroxylamine<br />
titration method. This is the amount of formaldehyde left unreacted<br />
with phenol in the resin at the end of synthesis. A lower number is preferred<br />
for higher resin use efficiency <strong>and</strong> lower emissions.<br />
4.7.5 pH<br />
The pH measures the basicity of the resin. A certain basic pH should be<br />
preferably maintained for the resin to be free of precipitation <strong>and</strong> to have a<br />
high water tolerance.<br />
4.7.6 Solids Content<br />
The solids content measures the concentration of the phenolic resin which<br />
is not evaporable at the test temperature for the duration of the test. The<br />
phenolic resin placed in an aluminum dish <strong>and</strong> is kept in a 150°C oven for<br />
2 hours.<br />
4.7.7 o-Cresol Contact Allergy<br />
The presence of o-cresol was established as a contact sensitizer in a phenol/formaldehyde<br />
resin. 74<br />
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5<br />
Urea/formaldehyde Resins<br />
Urea/formaldehyde glue resins are the most important type of urea/formaldehyde-resins.<br />
Monographs on the chemistry of urea/formaldehyde resins<br />
include those by Dunky, Meyer <strong>and</strong> Pizzi, Dijk. 1–4<br />
The industrial production of urea/formaldehyde glue resins for the<br />
wood-working industry started in 1931. Environmental concerns dem<strong>and</strong>ed<br />
a change of the formulation of urea/formaldehyde-resins to decrease the<br />
molar ratio of formaldehyde to urea to avoid formaldehyde emissions.<br />
5.1 HISTORY<br />
The reaction of urea with formaldehyde was first noted in 1884, with commercial<br />
interest in the polymers commencing at about 1918 with a patent<br />
issued to Hanns John (1891–1942). 5–7 However, in 1896 Carl Goldschmidt<br />
described precipitates formed when aqueous solutions of urea <strong>and</strong> formaldehyde<br />
were reacted under acidic conditions. 8 It is believed that the<br />
primary precipitate formed by Goldschmidt <strong>and</strong> empirically identified as<br />
C 5 H 10 O 3 N 4 was, in fact, a cyclically structured condensation product. 9<br />
5.2 SYNTHESIS OF RESIN<br />
5.2.1 Formaldehyde<br />
Formaldehyde is available in many forms. Paraform (solid, polymerized<br />
formaldehyde) <strong>and</strong> formalin solutions (aqueous solutions of formaldehyde,<br />
283
284 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
sometimes with methanol, in 37%, 44%, or 50% formaldehyde concentrations)<br />
are commonly used forms. Formaldehyde is also available as a gas.<br />
Typically, formalin solutions are the preferred source of formaldehyde.<br />
5.2.2 Urea<br />
Solid urea, such as prill, <strong>and</strong> urea solutions, typically aqueous solutions,<br />
are commonly available. Further, urea may be combined with another moiety,<br />
typically formaldehyde, often in an aqueous solution.<br />
5.2.3 Ammonia<br />
Ammonia is used to reduce the free formaldehyde content. Ammonia is<br />
available in various gaseous <strong>and</strong> liquid forms, particularly including aqueous<br />
solutions at various concentrations. Any of the commercially-available<br />
aqueous ammonia-containing solutions are the preferred form.<br />
Such solutions typically contain between 10 to 35% ammonia. A<br />
solution having 35% ammonia can be used, providing stability <strong>and</strong> control<br />
problems can be overcome. An aqueous solution containing about 28%<br />
ammonia is particularly preferred.<br />
Ammonia or late additions of urea are commonly used to reduce free<br />
formaldehyde levels in urea/formaldehyde polymer systems. Ammonia<br />
reduces the cured polymers’ resistance to hydrolysis. The addition of urea<br />
tends to produce a polymer that releases smoke during the cure cycle. 10<br />
5.2.4 Diketones<br />
Small additions of acetylacetone <strong>and</strong> ammonia to urea/formaldehyde resin<br />
can bind the free formaldehyde. 11 The addition causes the formation<br />
of 2,6-dimethyl-3,5-diacetyl-1,4-dihydropyridine (3,5-diacetyl-1,4-dihydrolutidine)<br />
by a Hantz reaction, as shown in Figure 5.1.<br />
5.2.5 Specialities<br />
5.2.5.1 Cationic Urea Formaldehyde Resins<br />
A water soluble cationic resin is prepared by initially reacting urea <strong>and</strong><br />
formaldehyde at a formaldehyde to urea mole ratio of 2 to 3 together with<br />
triethanolamine in a urea to triethanolamine mole ratio of 2 to 3. The<br />
resin formed is made cationic by acidifying it to a pH of 1.5, with a strong
Urea/formaldehyde Resins 285<br />
CH 3<br />
C O<br />
CH 2<br />
C O<br />
CH 3<br />
CH 2 O, NH 4 OH<br />
H 3 C<br />
H N<br />
H 3 C<br />
CH 3<br />
C<br />
O<br />
O<br />
C<br />
CH 3<br />
Figure 5.1: Binding of Formaldehyde by Acetylacetone<br />
inorganic acid such as hydrochloric, sulfuric, or nitric acid, followed by<br />
prompt neutralization to a pH of 6 to 7. A pH above 7 is discouraged as<br />
this retards the cure of the resin.<br />
Cationic urea formaldehyde resins with polymers containing vinylamine<br />
units improve the properties of paper with respect to dry strength<br />
<strong>and</strong> wet strength. 12<br />
Suitable polymers containing polymerized vinylamine units can be<br />
prepared by hydrolysis of homopolymers <strong>and</strong> copolymers containing polymerized<br />
N-vinylamide units.<br />
Examples for such polymers are a homopolymer of N-vinylformamide<br />
<strong>and</strong> a copolymer of methacrylic acid <strong>and</strong> N-vinylformamide. The<br />
amide group is often only partly hydrolyzed, say to an extent of 25%. The<br />
cationic urea/formaldehyde resins are infinitely dilutable with water.<br />
Aqueous solutions of cationic urea/formaldehyde resins typically<br />
have a solid content between 25 <strong>and</strong> 45%. The aqueous resin solutions or<br />
the solid products obtained therefrom are used as additives for increasing<br />
the dry <strong>and</strong> wet strength of paper in papermaking. The resins, in the form<br />
of aqueous solutions, are added to the paper stock prior to sheet formation.<br />
Water-soluble Resins. Water-soluble cationic urea/formaldehyde resins<br />
are obtained by condensing urea <strong>and</strong> formaldehyde in the presence of polyamines.<br />
The reactants are first precondensed in alkaline pH range, then condensed<br />
in acidic pH range until gel formation begins. They are subjected to<br />
post-condensation, for example, with formaldehyde, <strong>and</strong> are subsequently<br />
neutralized. 12
286 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
5.2.5.2 Melamine-modified Resins<br />
Urea is the st<strong>and</strong>ard nitrogen-containing component in urea/formaldehyde<br />
resins. Resins with improved properties can be obtained by substitution of<br />
the urea with melamine. Sulfitation of the methylol groups can improve the<br />
resin properties. Still another approach is the co-condensation with amines<br />
<strong>and</strong> the introduction of urea-terminated amines. Melamine improves the<br />
resistance against attack by humidity <strong>and</strong> water, especially at elevated temperatures.<br />
Melamine contents up to 25% are used. 1,1,2,2-Tetramethoxyethane<br />
(TME) is a high boiling point diacetal (165°C). It can be synthesized<br />
from glyoxal. Such acetals improve the performance of melamine/urea/-<br />
formaldehyde resins. The acetal as cosolvent increases the solubility of<br />
both the unreacted melamine <strong>and</strong> the oligomers in water. Thus a more effective<br />
reaction can be achieved. 13 The improvement of mechanical properties<br />
by the addition of acetals such as methylal <strong>and</strong> ethylal occurs because<br />
of the by increased effectiveness <strong>and</strong> participation of the melamine to the<br />
crosslinking reactions. 14<br />
Iminoamino methylene base intermediates are obtained by the decomposition<br />
of hexamethylenetetramine in the presence of strong anions<br />
such as SO 2−<br />
4<br />
<strong>and</strong> HSO − 4<br />
. These compounds improve the weathering resistance<br />
of hardened melamine/urea/formaldehyde resins. 15<br />
5.2.6 Polymerization<br />
The synthesis of a urea/formaldehyde (UF) resin proceeds via the methylolation<br />
of urea <strong>and</strong> condensation of the methylol groups. The reaction<br />
can be conducted in an aqueous medium because of the good solubility<br />
of both urea <strong>and</strong> formaldehyde. The basic reactions are shown in Figure<br />
5.2. The methylolation of urea is done in alkaline or slightly acidic<br />
solution in a two-fold excess of formaldehyde. Following methylolation,<br />
further condensation into methylene urea oligomers occurs, with a degree<br />
of oligomerization of 4 to 8. Because of the functionality of the nitrogen,<br />
branched products can be formed. Ether bridges also may be formed.<br />
These ether bridges can be rearranged into methylene bridges, expelling<br />
formaldehyde. Dimethylol urea is not a stable compound. In the presence<br />
of another formaldehyde reactive compound, dimethylol urea will donate<br />
its two formaldehyde groups to the more stable phenol, ammonia, melamine,<br />
etc. This leaves raw urea in the resin which reduces the durability<br />
significantly. 10
Urea/formaldehyde Resins 287<br />
O<br />
C<br />
H 2 N NH 2<br />
+<br />
H 2 C O C<br />
H 2 N NH CH 2 OH<br />
O<br />
O<br />
C<br />
H 2 N NH CH 2 OH<br />
O<br />
C<br />
O<br />
C<br />
H 2 N NH CH 2 O CH 2 N NH 2<br />
O<br />
O<br />
C<br />
C<br />
H 2 N NH CH 2 N NH 2<br />
Figure 5.2: Basic Reactions of Urea <strong>and</strong> Formaldehyde
288 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 5.1: Feed for a Urea Formaldehyde Resin 16<br />
Reactant<br />
mol<br />
Formalin solution, 50% CH 2 O 14.5<br />
Ethylene diamine 0.3<br />
Urea (first charge) 12.1<br />
NH 4 OH, 28% 6.1<br />
UFC 85: water a 14.4<br />
CH 2 O 34.5<br />
Urea 7.2<br />
Urea (second charge) 3.5<br />
Alum (KAlSO 4 × 12H 2 O) 50% 0.2<br />
NaOH 25% 0.02<br />
Latent catalyst 0.02<br />
Water 1.6<br />
a : 25% urea, 60% formaldehyde <strong>and</strong> 15% water<br />
5.2.6.1 UF three-step preparation<br />
The resin is prepared by reacting urea <strong>and</strong> formaldehyde in a three-step<br />
process.<br />
1. Urea <strong>and</strong> formaldehyde are reacted in the presence of ammonia,<br />
at an excess formaldehyde of 1.2 to 1.8. A cyclic triazone/triazine<br />
polymer is formed at 85 to 95°C within 2 hours.<br />
2. A thermosetting polymer is formed from the cyclic polymer. To<br />
the reaction mixture containing triazole/triazine polymer, an additional<br />
portion of formaldehyde is added, preferably with additional<br />
urea, to yield a higher cumulative F/U mole ratio of 2 to 2.7. The<br />
pH is adjusted to 6.0 to 6.4.<br />
3. If the resin is not used immediately, a third neutralization step<br />
should be employed, preferably with sodium hydroxide.<br />
Use of ammonia or late additions of urea are common techniques<br />
for reducing free formaldehyde content of urea/formaldehyde polymer systems.<br />
5.2.6.2 Synthesis Procedure<br />
An example of a synthesis procedure is given here. The reactants that are<br />
used to prepare a urea/formaldehyde resin are listed in Table 5.1. The re-
Urea/formaldehyde Resins 289<br />
sin is prepared by charging the 50% formalin, ethylene diamine, <strong>and</strong> urea<br />
into a reactor <strong>and</strong> heating the mixture to 45°C to dissolve the urea. Then<br />
NH 4 OH is added which causes the mixture to have an exothermic reaction<br />
reaching a temperature of 83°C. The reaction mixture is heated further to<br />
95°C <strong>and</strong> maintained at that temperature for 90 minutes. A cyclic polymer<br />
is formed in this initial phase of the chemical reaction. The triazone<br />
concentration can be over 50% of the total polymer mix at this stage of<br />
the synthesis, depending on the molar ratios of the ingredients. The pH<br />
of the mixture is maintained between 8.7 <strong>and</strong> 9.3 by adding 25% NaOH<br />
as needed ( a total of 0.4 mol). The reaction mixture is then cooled to<br />
85°C. UFC 85 (25% urea, 60% formaldehyde, <strong>and</strong> 15% water) <strong>and</strong> a second<br />
charge of urea are added to the reaction mixture. The temperature<br />
is thereafter maintained at 85°C for 10 minutes. The pH is adjusted from<br />
about 6.2 to 6.4 by adding a total of 0.2 mol of alum (KAlSO 4 ×12H 2 O) in<br />
increments over a course of 25 minutes. The reaction mixture was cooled<br />
to 80°C, <strong>and</strong> after 15 minutes, further cooled to 75°C. After 7 minutes, the<br />
reaction mixture is cooled to 55°C, 26.9 g 25% NaOH is added, <strong>and</strong> then<br />
the mixture is further cooled to 35°C. A latent catalyst was added <strong>and</strong> the<br />
reaction mixture is cooled to 25°C. The pH is finally adjusted to 7.6 to 8.2<br />
with 25% NaOH. The free formaldehyde content of the resin is 0.59%. After<br />
24 hours the free formaldehyde content drops to 0.15%. The viscosity<br />
of the resin is 573 cP.<br />
5.2.6.3 Cyclic Melamine/urea/formaldehyde Prepolymer<br />
Cyclic urea prepolymers may be used as modifiers of thermosetting phenol/formaldehyde<br />
<strong>and</strong> melamine/formaldehyde-based resins for a variety of<br />
end uses. These prepolymers are urea/formaldehyde polymers containing<br />
at least 20% triazone <strong>and</strong> substituted triazone compounds. The use of cyclic<br />
urea prepolymer in such resin binders provides properties superior to<br />
those obtained from using the resin alone, in many applications. The resins<br />
are modified with the cyclic urea prepolymer, either by reacting into<br />
the base resin system, blending with the completed base resin system, or<br />
blending into a binder preparation. Suitable primary amines can be used in<br />
the formulation, such as methylamine, ethylamine, <strong>and</strong> propylamine, ethanolamine,<br />
cyclopentylamine, ethylene diamine, hexamethylene diamine,<br />
<strong>and</strong> linear polyamines.<br />
A methylolated cyclic urea prepolymer is typically prepared by re-
290 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
acting urea, ammonia, <strong>and</strong> formaldehyde <strong>and</strong> then reacting with 2 mol of<br />
formaldehyde to produce a methylolated cyclic urea prepolymer having<br />
50% solids. 13 C-NMR indicates that 42.1% of the urea is contained in the<br />
triazone ring structure, 28.5% of the urea was di/tri-substituted, 24.5% of<br />
the urea is mono-substituted, <strong>and</strong> 4.9% of the urea is free. This cyclic urea<br />
prepolymer is then reacted into a st<strong>and</strong>ard phenol/formaldehyde resin during<br />
the cook cycle of the phenol/formaldehyde resin. In many systems, a<br />
cyclic prepolymer is either cooked into the resin or added to a resin. 10<br />
5.2.7 Manufacture<br />
The production of UF resins is usually achieved in three stages. 3<br />
1. Methylolation: urea reacts with aqueous formaldehyde under alkaline<br />
conditions at temperatures up to 100°C.<br />
2. Condensation: the condensation of methylols in slightly acidic<br />
medium yields oligomers with different molar mass <strong>and</strong> various<br />
functionalities. The condensation is then stopped by adding alkaline<br />
substances.<br />
3. Post treatment: evaporation of excess water <strong>and</strong> formaldehyde, or<br />
addition of secondary urea to decrease the ratio of formaldehyde<br />
to urea.<br />
The multistage process is useful to fulfill the requirements of retaining<br />
the reactivity <strong>and</strong> the strength of the cured resin under the condition of<br />
minimal emission of formaldehyde during service.<br />
5.3 SPECIAL ADDITIVES<br />
5.3.1 Modifiers<br />
A requirement is that the additives does not increase the viscosity of the<br />
suspension significantly, but would improve the toughness <strong>and</strong> the moisture<br />
resistance of UF resin. Thermoplastic acrylic copolymers with different<br />
degrees of hydrophilicity were added to a UF resin. The copolymers consist<br />
of two or three monomers selected from methyl methacrylate, acrylamide,<br />
acrylic acid, 1-vinyl-2-pyrrolidinone, ethyl acrylate, <strong>and</strong> vinyl acetate.<br />
The SEM micrographs of cured thermoplastic-modified UF showed<br />
a phase-separated thermoplastic structure in a continuous UF phase when
Urea/formaldehyde Resins 291<br />
Table 5.2: Global Production/Consumption Data of Important Monomers<br />
<strong>and</strong> <strong>Polymers</strong> 17<br />
Monomer Mill. Metric tons Year Reference<br />
Urea 110 2002<br />
18<br />
Formaldehyde 24 2003<br />
19<br />
Amino resins 8.4 2002<br />
20<br />
UF was modified with a self-dispersed <strong>and</strong> surfactant-stabilized polymer<br />
type. However, when the UF was modified with a water-soluble polymer,<br />
a single phase was detected.<br />
21, 22<br />
A water soluble, styrene-maleic anhydride copolymer can be used a<br />
modifier for binder resins. Glass fiber mats made with the modified binder<br />
composition exhibit an enhanced wet tensile strength, wet mat strength,<br />
tear strength, <strong>and</strong> dry tensile strength. Because of this strength improvement,<br />
the mat processing speeds through the cure oven can be significantly<br />
increased without risking breakage of the continuous mat. 23<br />
5.3.2 Flame Retardants<br />
As flame retardants, ammonium hydrogenphosphate ((NH 4 ) 2 HPO 4 ) <strong>and</strong><br />
sodium tetraborate (Na 2 B 4 O 7 ) were tested together with mineral fillers<br />
such as vermiculite, phlogopite, clay, etc. The increased flame resistance<br />
results from the evolution of noncombustible gases. 24<br />
5.3.3 Production Data of Important Monomers<br />
Production data of important raw materials are shown in Table 5.2. Urea is<br />
mostly used as a fertilizer. Only a small fraction is used for urea/formaldehyde<br />
resins. Formaldehyde is used not exclusively for urea/formaldehyde<br />
resins. Other major uses are phenol/formaldehyde resins, polyacetal resins,<br />
pentaerythritol 1,4-butanediol <strong>and</strong> hexamethylenetetramine. Amino resins<br />
include melamine/formaldehyde resins <strong>and</strong> melamine/urea/formaldehyde<br />
resins, besides urea/formaldehyde resins.<br />
5.4 CURING<br />
During curing, an insoluble, infusible, three-dimensional network is constructed.<br />
Curing is initiated by lowering the pH. This is achieved by the ad-
292 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
N<br />
H 2 C O<br />
+<br />
(NH 4 ) 2 SO 4<br />
N<br />
N<br />
+<br />
H 2 SO 4<br />
N<br />
Figure 5.3: Reaction of Ammonium Sulfate with Formaldehyde<br />
dition of acids, such as phosphoric acid or maleic acid. Acidic salts, e.g.,<br />
aluminum sulfate, or urea phosphate can be added. Further anhydrides,<br />
such as maleic anhydride, decompose in aqueous medium into acids. Ammonium<br />
sulfate reacts with formaldehyde to form hexamethylenetetramine<br />
<strong>and</strong> sulfuric acid, as shown in Figure 5.3.<br />
Ammonium chloride is now avoided for acidification in favor of ammonium<br />
sulfate. Residual ammonium chloride forms hydrochloric acid<br />
during the combustion of wood-based panels. It is suspected that the chlorine<br />
promotes the formation of chlorodioxins. Usually 2 to 3% of ammonium<br />
salt-based on the solid content of resin are sufficient as catalyst. Excess<br />
catalyst causes over-curing. Brittle resins are then formed, with less water<br />
resistance. Formaldehyde is the primary reactive component in urea/formaldehyde<br />
resins.<br />
A higher reactivity <strong>and</strong> a higher crosslinking density of the final network<br />
formation can be achieved by a higher formaldehyde-to-urea ratio.<br />
On the other h<strong>and</strong>, free formaldehyde is undesirable for toxicological reasons.<br />
Resins with very low formaldehyde content exhibit several drawbacks<br />
of the final product. These can be minimized, however by a special<br />
condensation process, the use of special accelerators, <strong>and</strong> by the modification<br />
of the formulation with melamine.<br />
5.5 MEASUREMENT OF CURING<br />
Curing can be monitored by thermal methods, as well as utilizing spectroscopic<br />
methods. The curing reaction in an ammonium chloride catalyzed<br />
system starts at around 100°C, whereas in an uncatalyzed system the curing<br />
reaction starts between 120 to 180°C. 25 In comparison to PF resins, the<br />
activation energy of curing of UF resins is generally higher. Nevertheless,
Urea/formaldehyde Resins 293<br />
the curing rates of UF resins are faster. 26 The pH values in UF formulations<br />
have a significant influence on the rate constants, but they affect the<br />
activation energy of curing marginally.<br />
The curing reaction in the presence of wood has been measured using<br />
15 N-distortionless enhancement by polarization transfer nuclear magnetic<br />
resonance spectroscopy (DEPT NMR). 27 A DEPT pulse sequence<br />
was employed to follow the curing of urea/formaldehyde resin.<br />
5.6 PROPERTIES<br />
5.6.1 Formaldehyde Release<br />
Typically, when urea/formaldehyde resins are cured, they release formaldehyde<br />
into the environment. Formaldehyde can also be released from the<br />
cured resin, particularly when the cured resin is exposed to acidic environments.<br />
Such formaldehyde release is undesirable, particularly in enclosed<br />
environments. Formaldehyde is malodorous <strong>and</strong> is considered hazardous<br />
to human <strong>and</strong> animal health. Various techniques have been used to reduce<br />
formaldehyde emission from urea/formaldehyde resins.<br />
Use of formaldehyde scavengers <strong>and</strong> methods for resin formulation,<br />
including addition of urea as a reactant late in the resin formation reaction,<br />
are techniques used to reduce formaldehyde emission. However, the use<br />
of formaldehyde scavengers often is undesirable, not only because of the<br />
additional cost, but also because it affects the properties, of the resin. For<br />
example, using ammonia as a formaldehyde scavenger reduces the resistance<br />
of the cured resin to hydrolysis. Later addition of urea to reduce free<br />
formaldehyde concentration in the resin generally yields a resin that must<br />
be cured at a relatively low rate to avoid smoking. The stability of the resin<br />
can also be adversely affected by such treatments. 16 Instead of urea,<br />
triethanolamine can be added to a mixture of urea <strong>and</strong> formaldehyde.<br />
5.6.2 Storage<br />
During storage, urea/formaldehyde resins undergo reactions that result in<br />
structural changes. Methylene groups adjacent to secondary amino groups<br />
are formed by the main reaction. This reaction proceeds between the free<br />
terminal hydroxymethyl <strong>and</strong> amino groups. 28
294 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
5.7 APPLICATIONS AND USES<br />
5.7.1 Glue Resins<br />
The main application of urea/formaldehyde resins is in the adhesive industry.<br />
Urea/formaldehyde glues are used in pressed wood products such<br />
as particle board, <strong>and</strong> plywood as laminating resins. Because of the potential<br />
for formaldehyde release, UF resins have been modified for indoor<br />
applications. Formaldehyde is a potent primary irritant.<br />
5.7.2 Binders<br />
Typical binders used to bind glass fiber mats include urea/formaldehyde<br />
resins, phenolic resins, melamine resins, bone glue, polyvinyl alcohols,<br />
<strong>and</strong> latices. These binder materials are impregnated directly into the fibrous<br />
mat <strong>and</strong> set or cured by heating to obtain the desired integrity in<br />
glass fibers. The most widely used glass mat binder is urea/formaldehyde,<br />
because it is relatively inexpensive. 16<br />
5.7.3 Foundry S<strong>and</strong>s<br />
In the manufacturing of low nitrogen-containing foundry s<strong>and</strong>s, the hexamine<br />
crosslinker is replaced partly with another crosslinking agent that<br />
does not contain nitrogen. Nitrogen, when present in coated foundry s<strong>and</strong><br />
can give rise to nitrogen defects during steel casting. It is preferable to<br />
have as low of nitrogen content as possible. Usually this other crosslinking<br />
agent is a thermosetting resol phenol/formaldehyde resin. During the<br />
manufacturing of low nitrogen-containing s<strong>and</strong>s, a novolak resin is added,<br />
followed by the resol resin <strong>and</strong> then the hexamine. 10<br />
5.8 SPECIAL FORMULATIONS<br />
5.8.1 Ready-use Powders<br />
For small scale applications, e.g., as adhesive, ready-use powders of urea/formaldehyde<br />
resins are dissolved in water. The formulation contains<br />
fillers, extenders, hardeners, scavengers, <strong>and</strong> other additives which have to<br />
be mixed with water only.
Urea/formaldehyde Resins 295<br />
5.8.2 Cyclic Urea Prepolymer in PF Laminating Resins<br />
Phenol/formaldehyde resins used to manufacture high pressure laminates<br />
are typically produced by reacting phenol <strong>and</strong> formaldehyde by means of<br />
an alkaline catalyst such as sodium hydroxide. 10<br />
Typical mole ratios of formaldehyde to phenol range from 1.2 to 1.9<br />
mol of formaldehyde per mol of phenol. Catalyst levels range from 0.5 to<br />
3%.<br />
The materials are reacted to a suitable endpoint, cooled under vacuum,<br />
<strong>and</strong> usually distilled to remove the water present from the formaldehyde<br />
solution as well as the water of condensation from the polymerization<br />
reaction. They may be used in this state or an organic solvent such as methanol<br />
can be added to reduce the solids concentration <strong>and</strong> viscosity of the<br />
mixture.<br />
A cyclic urea prepolymer in phenol-formaldehyde resins acts as a<br />
plasticizer for the resin. This makes the laminate more post-formable <strong>and</strong><br />
tougher. Products produced with such resins resist chipping <strong>and</strong> breakage<br />
during machining steps. Diluting the phenol-formaldehyde resin with<br />
cyclic urea prepolymer reduces the free phenol <strong>and</strong> other volatile phenolic<br />
moiety levels of the phenol-formaldehyde resin which reduces air pollution.<br />
Because of the plasticizing effect achieved with the cyclic urea prepolymer,<br />
higher F/P mole ratio PF resins (traditionally more brittle) can be<br />
used which further reduces the free phenol <strong>and</strong> volatile phenolic moiety<br />
levels.<br />
5.8.3 Liquid Fertilizer<br />
Urea/formaldehyde-based liquid fertilizers can provide nitrogen to the soil.<br />
In addition to nitrogen, phosphorous <strong>and</strong> potassium are considered major<br />
nutrients essential for plant growth. Long-term stability of high nitrogen<br />
liquid urea/formaldehyde fertilizers can be achieved by forming either a<br />
high percentage (more than 30%) of cyclic triazone structures or by condensing<br />
the urea/formaldehyde resin into small urea/formaldehyde polymer<br />
chains. 29<br />
5.8.4 Soil Amendment<br />
Urea/formaldehyde resin foams are used as a soil amendment for agricultural<br />
applications. The amendment by UF foams does not influence the pH
296 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
<strong>and</strong> causes insignificant alterations to the physical properties of the soil by<br />
slightly increasing total porosity, water availability, <strong>and</strong> the porosity, <strong>and</strong><br />
by reducing the bulk density. 30<br />
5.8.5 Microencapsulation<br />
Self-healing polymers <strong>and</strong> composites with microencapsulated healing agents<br />
offer a possibility for long-lived polymeric materials. Healing agents<br />
have been microencapsulated using urea/formaldehyde resins. The microcapsules<br />
must have sufficient strength to remain intact during polymer processing.<br />
However, the microcapsules should break when the polymer is<br />
damaged. 31<br />
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Polym. Sci., 87(6):898–907, February 2003.
298 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
23. S.-G. Chang, L. R. Graves, C. R. Hunter, <strong>and</strong> S. L. Wertz. Modified ureaformaldehyde<br />
binder for making fiber mats. US Patent 6 084 021, assigned<br />
to Georgia-Pacific Resins, Inc. (Atlanta, GA), July 4 2000.<br />
24. A. N. Egorov, Y. I. Sukhorukov, G. V. Plotnikova, <strong>and</strong> A. K. Khaliullin. Fireproofing<br />
coatings based on urea resins for metallic structures. Russ. J. Appl.<br />
Chem., 75(1):152–155, January 2002.<br />
25. J. Lisperguer <strong>and</strong> C. Droguett. Curing characterization of urea formaldehyde<br />
resins by differential scanning calorimetry (DSC). Bol. Soc. Chilena Quim.,<br />
47(1):33–38, March 2002.<br />
26. G. B. He <strong>and</strong> B. Riedl. Phenol-urea-formaldehyde cocondensed resol resins:<br />
Their synthesis, curing kinetics, <strong>and</strong> network properties. J. Polym. Sci., Part.<br />
B: Polym. Phys., 41(16):1929–1938, August 2003.<br />
27. B. D. Gill, M. Manley-Harris, <strong>and</strong> R. A. Thomson. Use of natural abundance<br />
15 N DEPT NMR to investigate curing of urea-formaldehyde resin in<br />
the presence of wood fibers. Magn. Reson. Chem., 41(8):622–625, August<br />
2003.<br />
28. P. Christjanson, K. Siimer, T. Pehk, <strong>and</strong> I. Lasn. Structural changes in urea-formaldehyde<br />
resins during storage. Holz als Roh- und Werkst., 60(6):<br />
379–384, December 2002.<br />
29. K. D. Gabrielson. Controlled release urea-formaldehyde liquid fertilizer resins.<br />
US Patent 6 632 262, assigned to Georgia-Pacific Resins, Inc. (Atlanta,<br />
GA), October 14 2003.<br />
30. P. A. Nektarios, A.-E. Nikolopoulou, <strong>and</strong> I. Chronopoulos. Sod establishment<br />
<strong>and</strong> turfgrass growth as affected by urea-formaldehyde resin foam soil<br />
amendment. Scientia Horticulturae, 100(1-4):203–213, March 2004.<br />
31. E. N. Brown, M. R. Kessler, N. R. Sottos, <strong>and</strong> S. R. White. In situ poly(ureaformaldehyde)<br />
microencapsulation of dicyclopentadiene. J. Microencapsul.,<br />
20(6):719–730, November–December 2003.
6<br />
Melamine Resins<br />
Melamine resins rely on 1,3,5-triazine-2,4,6-triamine <strong>and</strong> formaldehyde.<br />
They are similar to urea formaldehyde polymers.<br />
6.1 HISTORY<br />
The industrial use of melamine resin started in the late 1930s when the<br />
Swiss company CIBA began the industrial production of melamine from<br />
dicy<strong>and</strong>iamide. 1, 2 Earlier, the use of this resin was limited because of its<br />
high price. Now melamine can be produced cheaper from urea, so the<br />
economical situation is improved.<br />
6.2 MONOMERS<br />
6.2.1 Melamine<br />
Melamine may be partially or totally replaced with other suitable aminecontaining<br />
compounds. Alternatives to melamine include urea, thiourea,<br />
dicy<strong>and</strong>iamide, 2,5,8-triamino-1,3,4,6,7,9,9b-heptaazaphenalene (melem),<br />
(N-4,6-diamino-1,3,5-triazin-2-yl)-1,3,5-triazine-2,4,6-triamine (melam),<br />
melon, ammeline, ammelide, substituted melamines, <strong>and</strong> guanamines. 3<br />
The melamine homologues melam, melem, <strong>and</strong> melon have higher thermal<br />
stability than pure melamine. These compounds are also used as flame<br />
retardants.<br />
299
300 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Substituted melamines include alkyl melamines <strong>and</strong> aryl melamines.<br />
Representative examples of some alkyl-substituted melamines include<br />
methylmelamine, dimethylmelamine, trimethylmelamine, ethylmelamine,<br />
<strong>and</strong> 1-methyl-3-propyl-5-butylmelamine. Typical examples of an<br />
aryl-substituted melamine are phenylmelamine or diphenylmelamine. Melamine<br />
<strong>and</strong> related compounds are shown in Figure 6.1. Foams <strong>and</strong> fibers<br />
exhibit increased elasticity, when some of the melamine is replaced by<br />
a substituted melamine, e.g., N-mono-, N,N ′ -bis- <strong>and</strong> N,N ′ ,N ′′ -tris(5-hydroxy-3-oxapentyl)melamine.<br />
4 However, based on considerations of cost<br />
<strong>and</strong> availability, st<strong>and</strong>ard melamine is generally preferred.<br />
6.2.2 Other Modifiers<br />
Suitable resin modifiers are ethylene diamine, melamine, ethylene ureas,<br />
<strong>and</strong> primary, secondary, <strong>and</strong> tertiary amines. Dicy<strong>and</strong>iamide can be also<br />
incorporated into the resin.<br />
The concentrations of these modifiers in the reaction mixture may<br />
vary typically from 0.05 to 5.00%. All these modifiers promote hydrolysis<br />
resistance, polymer flexibility, <strong>and</strong> lower formaldehyde emissions. 5<br />
6.2.3 Synthesis<br />
Similar to urea, melamine reacts with formaldehyde in weakly alkalineaqueous<br />
media to form methylol compounds. Melamine is hexafunctional,<br />
so up to hexamethylol monomers can be formed. Hexamethylol melamine<br />
is shown in Figure 6.2.<br />
The further condensation proceeds under neutral <strong>and</strong> acidic conditions,<br />
thereby forming methylene or dimethylene ether bonds. A pure melamine<br />
resin gels within a few days at room temperature. Because of this<br />
undesired property, melamine resins are blended with urea resins.<br />
6.2.3.1 Etherified Resins<br />
Etherified resins are prepared by the reaction of melamine with formaldehyde<br />
under the conditions of pH around 6 <strong>and</strong> reflux temperature in the<br />
presence of a large amount of butanol. Xylene cycles out the water formed<br />
by the condensation reaction by azeotropic distillation <strong>and</strong> accelerates the<br />
etherification in this way.
Melamine Resins 301<br />
H<br />
H 2 N N NH 2<br />
N N<br />
NH 2<br />
H 2 N<br />
N<br />
N<br />
N<br />
NH 2<br />
N<br />
N<br />
N NH 2<br />
N<br />
NH 2<br />
Melamine<br />
Melam<br />
NH 2<br />
NH 2<br />
NH 2<br />
N<br />
N<br />
N<br />
N<br />
N<br />
N<br />
N<br />
N<br />
N<br />
N<br />
H 2 N<br />
N<br />
N<br />
H 2 N<br />
N<br />
N<br />
NH<br />
n<br />
Melem<br />
Melon<br />
H 2 N N NH 2<br />
N<br />
N<br />
Benzoguanamine<br />
H<br />
HH<br />
N N<br />
H<br />
C C<br />
N<br />
N<br />
H<br />
Dicy<strong>and</strong>iamide<br />
Figure 6.1: Melamine, Melam, Melem, Melon, Benzoguanamine, Dicy<strong>and</strong>iamide
302 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
H 2 N N NH 2<br />
H 2 C O<br />
N<br />
N<br />
+<br />
NH 2<br />
HOH 2 C<br />
N<br />
HOH 2 C<br />
N<br />
N<br />
CH 2 OH<br />
N<br />
CH 2 OH<br />
N<br />
HOH 2 C<br />
N<br />
CH 2 OH<br />
Figure 6.2: Hexamethylol melamine from Melamine <strong>and</strong> Formaldehyde<br />
6.2.4 Manufacture<br />
Melamine is mixed with neutralized formaldehyde solution. The excess<br />
of formaldehyde is about threefold. The mixture is heated to 75 to 85°C.<br />
When the solution becomes cloudy, water is admixed. Then fillers can be<br />
admixed for molding resins. The mixture is dried at 70 to 80°C. while the<br />
condensation reaction still proceeds.<br />
In the co-condensation of melamine <strong>and</strong> urea, due to the difference<br />
in reactivity of melamine <strong>and</strong> urea, the condensation of melamine moiety<br />
is quicker than the urea moiety.<br />
6.3 PROPERTIES<br />
Phenol/formaldehyde resins <strong>and</strong> melamine/formaldehyde resins are st<strong>and</strong>ard<br />
resins used for many products. The choice of resin depends on the<br />
desired properties. Phenol/formaldehyde resins are strong <strong>and</strong> durable <strong>and</strong><br />
relatively inexpensive, but are generally colored resins. Melamine resins<br />
are water clear but are more expensive. They are generally used for products<br />
where the color or pattern of the substrate is retained with a transparent
Melamine Resins 303<br />
melamine protective coating or binder.<br />
The emission of formaldehyde in melamine/urea/formaldehyde resins<br />
is decreased as the melamine content is increased. 6 This is explained<br />
due to the stronger bonding between triazine carbons of melamine than<br />
those of urea carbons. Sulfonated melamine/formaldehyde resins exhibit<br />
good solubility in water. 7<br />
6.4 APPLICATIONS AND USES<br />
Melamine based resins are widely used as adhesives for wood, as resins for<br />
decorative laminates, varnish, <strong>and</strong> moldings, <strong>and</strong> for improving the properties<br />
of paper <strong>and</strong> cellulosic textiles. In comparison to urea formaldehyde<br />
resins, a melamine-based resin has higher resistance against heat <strong>and</strong> moisture.<br />
Etherified melamine resins are often used in combination with alkyd<br />
resins for production of decorative laminates. Modification of textiles<br />
by melamine is used to impart crease resistance <strong>and</strong> shrinkage. The wet<br />
strength of paper is greatly improved by the use of melamine resins as<br />
wet-end additives.<br />
Acoustic ceiling tiles are backcoated with melamine resins in order<br />
to make them more rigid <strong>and</strong> humidity-resistant when installed in suspended<br />
ceilings. Melamine resins are also used for the preparation of decorative<br />
or overlay paper laminates. This application is due to their excellent<br />
color, hardness, <strong>and</strong> solvent, water, <strong>and</strong> chemical resistance, heat resistance,<br />
<strong>and</strong> humidity resistance.<br />
Molded articles, such as dinnerware, are prepared with a combination<br />
of melamine/formaldehyde resins <strong>and</strong> urea/formaldehyde resins. The<br />
resins are combined because the melamine/formaldehyde resin is too expensive<br />
by itself. The such articles made from these resins are generally<br />
not very water-resistant or dimensionally stable. 5<br />
6.4.1 Wood Impregnation<br />
Melamine/formaldehyde (MF) belongs to the hardest <strong>and</strong> stiffest isotropic<br />
polymeric materials used for decorative laminates, molding compounds,<br />
adhesives, coatings, <strong>and</strong> other products. Due the high hardness <strong>and</strong> stiffness,<br />
<strong>and</strong> low flammability, MF resins can be used to improve the properties<br />
of solid wood. An MF resin can penetrate the amorphous region of
304 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
wood. It has been established that significant portions of a suitable MF<br />
resin penetrate the secondary cell wall layers <strong>and</strong> middle lamella of softwoods.<br />
8<br />
6.5 SPECIAL FORMULATIONS<br />
6.5.1 Resins with Increased Elasticity<br />
In foams <strong>and</strong> fibers, with increased elasticity, the melamine is partly replaced<br />
by a hydroxy alkyl substituted melamine. To prepare these resins,<br />
melamine <strong>and</strong> substituted melamine are polycondensed together with<br />
formaldehyde. The feed may also contain small amounts of customary<br />
additives, such as disulfite, formate, citrate, phosphate, polyphosphate, urea,<br />
dicy<strong>and</strong>iamide, or cyanamide. 4 Moldings are produced by curing the<br />
resins in a conventional manner by adding small amounts of acids, preferably<br />
formic acid. Foams can be produced by foaming an aqueous solution<br />
or dispersion containing the melamine/formaldehyde precondensate,<br />
an emulsifier, a blowing agent <strong>and</strong> a curing agent.<br />
6.5.2 Microspheres<br />
Monodisperse melamine/formaldehyde microspheres have been prepared<br />
via a dispersed polycondensation technique. The nucleation <strong>and</strong> growth<br />
of the particles were achieved within short periods. A continuous coagulation<br />
occurred even in the presence of surfactants. 9 Microcapsules are<br />
interesting because of the controlled-release properties of the respective<br />
encapsulated substances. A fragrant oil could be microencapsulated by an<br />
in-situ polymerization. 10 The particle sizes ranged from 12 to 15 µm. The<br />
efficiency of encapsulation of the fragrant oil reached up to 67-81%.<br />
Microcapsules were prepared in a capillary flow microreactor <strong>and</strong><br />
also in a batch experiment. The microcapsules obtained from the microreactor<br />
showed smaller particle diameters <strong>and</strong> a narrower particle size distribution<br />
than those obtained in a batch experiment. 11<br />
REFERENCES<br />
1. M. Higuchi. Melamine resins (overview). In J. C. Salamone, editor, The<br />
Polymeric Materials Encyclopaedia: Synthesis, Properties <strong>and</strong> <strong>Applications</strong>,<br />
pages 837–838. CRC Press, Boca Raton, FL, 1999.
Melamine Resins 305<br />
2. Gesellschaft für Chemische Industrie in Basel. Verfahren zur Herstellung<br />
von 2.4.6-Triamino-1.3.5-triazin (Melamin). CH Patent 189 406, assigned to<br />
Ciba AG, February 28 1937.<br />
3. G. M. Crews, S. Ji, C. U. Pittman, Jr., <strong>and</strong> R. Ran. Ammeline-melamineformaldehyde<br />
resins (amfr) <strong>and</strong> method of preparation. US Patent 5 254 665,<br />
assigned to Melamine Chemicals, Inc. (Donaldsonville, LA), October 19<br />
1993.<br />
4. J. Weiser, W. Reuther, G. Turznik, W. Fath, H. Berbner, <strong>and</strong> O. Graalmann.<br />
Melamine resin moldings having increased elasticity. US Patent 5 162 487,<br />
assigned to BASF Aktiengesellschaft (Ludwigshafen, DE), November 10<br />
1992.<br />
5. F. C. Dupre, M. E. Foucht, W. P. Freese, K. D. Gabrielson, B. D. Gapud,<br />
W. H. Ingram, T. M. McVay, R. A. Rediger, K. A. Shoemake, K. K. Tutin,<br />
<strong>and</strong> J. T. Wright. Cyclic urea-formaldehyde prepolymer for use in phenolformaldehyde<br />
<strong>and</strong> melamine-formaldehyde resin-based binders. US Patent<br />
6 379 814, assigned to Georgia-Pacific Resins, Inc. (Atlanta, GA), April 30<br />
2002.<br />
6. S. Tohmura, A. Inoue, <strong>and</strong> S. H. Sahari. Influence of the melamine content<br />
in melamine-urea-formaldehyde resins on formaldehyde emission <strong>and</strong> cured<br />
resin structure. J. Wood Sci., 47(6):451–457, 2001.<br />
7. L. H. Su, S. R. Qiao, J. Xiao, X. Tang, G. D. Zhao, <strong>and</strong> S. W. Fu. Synthesis<br />
<strong>and</strong> properties of high-performance <strong>and</strong> good water-soluble melamine-formaldehyde<br />
resin. J. Appl. Polym. Sci., 81(13):3268–3271, September 2001.<br />
8. W. Gindl, F. Zargar-Yaghubi, <strong>and</strong> R. Wimmer. Impregnation of softwood<br />
cell walls with melamine-formaldehyde resin. Bioresour. Technol., 87(3):<br />
325–330, May 2003.<br />
9. I. W. Cheong, J. S. Shin, J. H. Kim, <strong>and</strong> S. J. Lee. Preparation of monodisperse<br />
melamine-formaldehyde microspheres via dispersed polycondensation.<br />
Macromol. Res., 12(2):225–232, April 2004.<br />
10. H. Y. Lee, S. J. Lee, I. W. Cheong, <strong>and</strong> J. H. Kim. Microencapsulation of<br />
fragrant oil via in situ polymerization: effects of ph <strong>and</strong> melamine-formaldehyde<br />
molar ratio. J. Microencapsul., 19(5):559–569, September–October<br />
2002.<br />
11. T. Sawada, M. Korenori, K. Ito, Y. Kuwahara, H. Shosenji, Y. Taketomi,<br />
<strong>and</strong> S. Park. Preparation of melamine resin micro/nanocapsules by using<br />
a microreactor <strong>and</strong> telomeric surfactants. Macromol. Mater. Eng., 288(12):<br />
920–924, December 2003.
7<br />
Furan Resins<br />
Furan resins are condensation products of furfuryl alcohol (FA). The resins<br />
are derived from vegetable cellulose, a renewable resource. 1 Furans as<br />
constituents of polymers have been reviewed. 2<br />
7.1 HISTORY<br />
In Latin, furfur means bran. Furfural was first isolated in 1832 (or 1821)<br />
by Döbereiner ∗ , as a by-product of the synthesis of formic acid. In 1840<br />
the ability of furfural to form resins was discovered by Stenhous. 3 The<br />
industrial production of furfural started in 1922, <strong>and</strong> one year later the first<br />
furan-based resins emerged. Early patents on furan resins include that of<br />
Claessen 4 <strong>and</strong> one for synthetic resins, (actually mixed phenol furan resins)<br />
suitable for use in molding gramophone records. 5<br />
7.2 MONOMERS<br />
Monomers suitable for furan resins are listed in Table 7.1. One of the chief<br />
advantages in furan resins stems from the fact that they are derived from<br />
vegetable cellulose. Suitable sources of vegetable cellulose are corn cobs,<br />
sugar cane bagasse, oat hulls, paper mill by-products, biomass refinery<br />
1849<br />
∗ Johann Wolfgang Döbereiner, born in Hof an der Saale 1780, in Germany, died in Jena<br />
307
308 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 7.1: Monomers for Furan Resins 6<br />
Furan Compound<br />
Remarks or Reference<br />
Furan<br />
Furfural<br />
Furfuryl alcohol<br />
5-Hydroxymethylfurfural (HMF)<br />
5-Methylfurfural<br />
2-Furfurylmethacrylate<br />
7<br />
Bis-2,5-hydroxymethylfuran Glass fiber binder<br />
2,5-Fur<strong>and</strong>icarboxylic acid<br />
O<br />
OH<br />
OH<br />
OH<br />
HO<br />
OH<br />
OH<br />
OH<br />
OH<br />
OH<br />
OH<br />
O<br />
C H<br />
O<br />
Figure 7.1: Mechanism of the Formation of Furfural<br />
eluents, cottonseed hulls, rice hulls, <strong>and</strong> food stuffs such as saccharides<br />
<strong>and</strong> starch. 6<br />
Pentoses hydrolyze to furfural <strong>and</strong> hexoses give 5-hydroxymethylfurfural<br />
on acid digestion. 8<br />
7.2.1 Furfural<br />
Furfuraldehyde is a by-product from the sugar cane bagasse which produces<br />
resins with an excellent chemical stability <strong>and</strong> low swelling. 2-Furan<br />
formaldehyde or furfural is made from agricultural materials by means of<br />
hydrolysis.<br />
The mechanism of formation of furfural is shown in Figure 7.1. It<br />
is a light yellow to amber colored transparent liquid. Its color gradually<br />
deepens to brown during storage. It tastes like apricot kernel. It is mainly
Furan Resins 309<br />
used in lubricant refinement, furfuryl alcohol production, <strong>and</strong> pharmaceutical<br />
production.<br />
Furfural is the chief reagent used to produce materials such as furfuryl<br />
alcohol, 5-hydroxymethylfurfural (HMF), bis(hydroxymethyl)furan<br />
(BHMF), <strong>and</strong> 2,5-dicarboxyaldehyde-furan. The furan-containing monomers<br />
in turn can undergo reactions to produce various furan-containing<br />
monomers with a wide variety of substituents as shown in Table 7.1.<br />
7.2.2 Furfuryl Alcohol<br />
Furfuryl alcohol is made from furfural by reduction with hydrogen. It is a<br />
colorless transparent liquid <strong>and</strong> becomes brown, light yellow, or deep red,<br />
when exposed in the air. It can be mixed with water <strong>and</strong> many organic solvents<br />
such as alcohol, ether, acetone, etc., but not in hydrocarbon products.<br />
7.2.3 Specialities<br />
7.2.3.1 Furan-based Polyimides<br />
Polyimides based on poly(2-furanmethanol-formaldehyde) can be prepared<br />
by a Diels-Alder reaction (DA) of the respective furan resin with bismaleimides.<br />
9 The Diels-Alder reaction proceeds in tetrahydrofuran (THF) or<br />
in bulk. The tetrahydrophthalimide intermediates aromatize in the presence<br />
of acetic anhydride. Polyimides based on the furan resin exhibit good<br />
thermal stability.<br />
7.2.4 Synthesis<br />
Furan-based monomers can polymerize through two well-known mechanisms.<br />
The first involves chain or polyaddition polymerization, which is<br />
initiated by free radical, cationic or anionic promoters. Polymerization<br />
produces macromolecules with furan rings pendant on the main chain.<br />
The second method is a polycondensation, also referred to as polymerization<br />
condensation. <strong>Polymers</strong> <strong>and</strong> copolymers resulting from acid<br />
catalyzed condensation reactions result in macromolecules with furan rings<br />
in the main chain. 6<br />
As a general rule, the furan resins formed by polycondensation reactions<br />
have stiffer chains <strong>and</strong> higher glass transition temperatures. These<br />
reactions may involve self-condensation of the furan monomers described
310 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
CH 2<br />
OH<br />
H +<br />
O<br />
CH 2<br />
+<br />
O<br />
CH 2<br />
+<br />
O<br />
CH 2<br />
OH<br />
O<br />
CH 2<br />
O<br />
CH 2<br />
OH<br />
Figure 7.2: Acid Catalyzed Self-condensation of Furfuryl Alcohol<br />
above, as well as condensation reactions of such monomers with aminoplast<br />
resins, organic anhydrides, <strong>and</strong> aldehydes such as formaldehyde, ketones,<br />
urea, phenol, <strong>and</strong> other suitable reagents. Most common, furan resins<br />
are produced by acid catalyzed condensation reactions.<br />
The condensation results in linear oligomers, the furan rings being<br />
linked with methylene <strong>and</strong> methylene-ether bridges, c.f. Figure 7.2.<br />
The synthesis of furan resins proceeds in a pH range of 3 to 5, at<br />
a temperature range of 80 to 100°C. The condensation is stopped, when a<br />
desired viscosity value is reached, by neutralizing the liquid resin.<br />
Furfuryl alcohol can also be condensed with formaldehyde to obtain<br />
furan-formaldehyde resins. The content of free formaldehyde can be<br />
lowered by the addition of urea at the late stages of synthesis.<br />
7.3 SPECIAL ADDITIVES<br />
7.3.1 Reinforcing Materials<br />
Aramid fibers were used as reinforcing material for a phenol resin <strong>and</strong> a<br />
furan resin. A comparative study of the mechanical performance of the<br />
materials showed that the furan resin is more suitable as a matrix than the<br />
phenol resin. 10
Furan Resins 311<br />
Table 7.2: Global Production Data of Furan Resins Related Components 11<br />
Monomer Mill. Metric tons Year Reference<br />
Formaldehyde 24 2003<br />
12<br />
Furfural 0.225 1999<br />
13<br />
7.3.2 Production Data of Important Monomers<br />
The most important industrial furan resins are based on 2-furfuryl alcohol.<br />
The largest producers of furfural are China <strong>and</strong> the Dominican Republic.<br />
Production data are shown in Table 7.2. Around 30% of the furfural consumption<br />
is used to produce furfuryl alcohol, which is mainly consumed<br />
by the production of furan resins.<br />
7.4 CURING<br />
Materials known to be suitable for curing furan resins include inorganic<br />
<strong>and</strong> organic acids. Examples of suitable organic <strong>and</strong> inorganic acids include<br />
hydrochloric acid, sulfuric acid, nitric acid, phosphoric acid, tartaric<br />
acid, <strong>and</strong> maleic acid. Friedel-Crafts catalysts include aluminum trichloride,<br />
zinc chloride, aluminum bromide, <strong>and</strong> boron fluoride.<br />
Resins with improved fire resistance are cured with a mixture of<br />
trimethylborate, boric anhydride, <strong>and</strong> p-toluenesulfonic acid. 14<br />
Salts of both inorganic <strong>and</strong> organic acids may also be used. Ammonium<br />
sulfate is preferred. Ammonium sulfate is a latent catalyst which may<br />
become active at approximately 110 to 150°C. Suitable organic salts are the<br />
urea salt of toluenesulfonic acid, the polyammonium salts of polycarboxylic<br />
acids such as the diammonium salts of citric acid, <strong>and</strong> the ammonium<br />
salts of maleic acid. Cyclic anhydrides such as maleic anhydride are also<br />
suitable for use as catalysts.<br />
It is believed that polyester co-polymers are formed between the anhydride<br />
<strong>and</strong> the free hydroxylated species present in the resin. Maleic<br />
acid promotes the polymerization reaction. Furthermore, it is believed that<br />
maleic acid may preferentially reduce the emission of bis(hydroxymethyl)furan<br />
monomer during the curing process. A significant reduction of<br />
volatile organic compounds (VOCs), will use a catalyst system comprised<br />
of maleic acid <strong>and</strong> ammonium sulfate. 6
312 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
O<br />
CH CH 2<br />
O<br />
CH 2<br />
O<br />
CH CH 2<br />
Figure 7.3: Crosslinked Methylene Bridges<br />
7.4.1 Acidic Curing<br />
The resin can be crosslinked by an acidic catalyst. The reaction is not<br />
sensitive to air. The main route of curing is an additional condensation reaction<br />
at the free α-hydrogen of furan rings. These positions are connected<br />
by methylene bridges.<br />
7.4.2 Oxidative Curing<br />
The oxidative crosslinking of furfuryl alcohol (FA) polycondensates proceeds<br />
at temperatures of 100 to 200°C. Structures with tertiary carbon<br />
atoms, as shown in Figure 7.3, could be identified.<br />
7.4.3 Ultrasonic Curing<br />
Ultrasonic treatment, i.e., sonication during the curing process of a furan<br />
resin, showed changes of the curing performance. p-Toluenesulfonic acid<br />
was added as curing catalyst in the proportion of 0.3%. Fine carbons were<br />
also incorporated.<br />
Using an ultrasonic homogenizer in the presence of carbonaceous<br />
fine particles showed an increased curing rate of the furan resin. This, in<br />
turn, increased the polymerization degree with an increase in ultrasound<br />
intensity. The increase of curing rate was also observed by small additions<br />
of carbonaceous fine particles. In this case, the curing accelerated with an<br />
increase in the specific surface area of the additives. 15<br />
The increase of curing rate is believed to result from cavitation. The<br />
curing reaction proceeds slowly in the absence of cavitation <strong>and</strong> simple<br />
stirring fails to produce such a marked increase in the rate of reaction. The<br />
curing is accelerated by heat, oxygen, <strong>and</strong> the addition of phenol <strong>and</strong> urea.
Furan Resins 313<br />
7.5 PROPERTIES<br />
7.5.1 Recycling<br />
Research has been conducted to introduce pendent furan groups into polymers<br />
such as poly(styrene) via copolymerization with a suitable comonomer.<br />
The pendent furan moieties can be crosslinked with a bismaleimide<br />
to achieve polymers with better performance. In order to recycle these<br />
crosslinked materials, heating experiments with an excess of 2-methylfuran<br />
were performed in order to induce the retro Diels-Alder reaction<br />
<strong>and</strong> break-up the network. The reaction proceeded in this manner <strong>and</strong> the<br />
original copolymers could be recovered from the treatment. Therefore,<br />
the introduction of furan units is a potential path of recycling crosslinked<br />
polymers by thermal treatment with a diene in excess. 16<br />
The Diels-Alder reaction between styrene-furfuryl methacrylate copolymer<br />
samples <strong>and</strong> bismaleimide can be monitored the ultraviolet absorbance<br />
of the maleimide group at 320 nm or by 13 C-NMR spectroscopy. 7<br />
7.6 APPLICATIONS AND USES<br />
Furan resins are used mainly in the foundry industry, as s<strong>and</strong> binders for<br />
casting molds <strong>and</strong> cores. Furan resins are often used in combination with<br />
other resins. Furan resins are highly corrosion resistant. Therefore, they<br />
have found use in mortars <strong>and</strong> in cements. Improved mechanical properties<br />
are implemented by reinforcing with glass fibers.<br />
7.6.1 Carbons<br />
Porous Carbon. Furan resins form a porous carbon by pyrolysis at 450°C.<br />
Glass-like Carbon. Glass-like carbon is identified as an excellent carbon<br />
artifact due to its characteristics such as hardness <strong>and</strong> shape stability. The<br />
microstructure of glass-like carbon consists of a non-graphitic alignment of<br />
hexagonal sheets. It has unique properties such as great hardness compared<br />
with other carbon materials <strong>and</strong> impermeability for gases. 17<br />
Glass-like carbon is of interest in the battery <strong>and</strong> semiconductor industries.<br />
Glass-like carbon is prepared by heat-treatment on thermosetting<br />
resins in inert atmosphere.
314 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Figure 7.4: SEM photographs of glass-like carbon derived from furan resin. (a)<br />
300, (b) 600 °C. 18 (Reprinted with permission from Elsevier)<br />
During the heat-treatment of a furan resin, weight loss is very rapid<br />
up to 500°C, then continues gradually up to 1000°C, <strong>and</strong> then the weight<br />
stays almost constant above 1000°C. SEM photographs of heat treated<br />
glass-like carbon reveal a large increase of micro-grain size in the range<br />
of 60 to 105 nm when treated at 2000°C. Up to 2500°C, the grain size<br />
decreases to 27 to 40 nm due to graphitization. 18 There is a structural<br />
correlation between the micro-texture of the furan resin <strong>and</strong> the glass-like<br />
carbon formed from the particular resin. The pore structure in glass-like<br />
carbon can be characterized by small-angle X-ray scattering (SAXS) technique.<br />
The scattering intensities grow gradually with increasing heat-treatment<br />
temperature up to 1600 to 1800°C, <strong>and</strong> then the intensities increase<br />
abruptly at a temperature higher than 1800°C.<br />
The dependence of the structural change of a glass-like carbon from<br />
a furan resin is almost the same as that of a phenolic resin. However, it<br />
was found that the carbon prepared at 1200°C from furan resin shows the<br />
largest interlayer spacing in the carbon matrix <strong>and</strong> at the same time the<br />
smallest value of the gyration radius for the pores. 17<br />
7.6.2 Chromatography Support<br />
Conventionally used packing materials for liquid chromatography are a<br />
chemically bonded type of packing material based on silica gel <strong>and</strong> a pack-
Furan Resins 315<br />
ing material based on synthetic resin. The silica gel-based packing material<br />
has relatively strong in mechanical properties <strong>and</strong> in its swelling or shrinking<br />
characteristics against various organic solvents. Therefore, it has a high<br />
resolving power <strong>and</strong> is superior in exchangeability of eluent for analysis.<br />
However, the silica gel-based packing material has problems in that the silica<br />
gel dissolves under acidic or alkaline conditions <strong>and</strong> the solubility of<br />
the silica gel in an aqueous solution increases when warmed, resulting in<br />
durability problems.<br />
The packing material of synthetic resin, on the other h<strong>and</strong>, is known<br />
to be high in acid- <strong>and</strong> alkali-resistivity, <strong>and</strong> has a good chemical durability<br />
as a packing material. However, since the mechanical strength of the particles<br />
is small, it has been difficult to convert them into finer particles. Raw<br />
materials which are highly chemically stable <strong>and</strong> exhibit high mechanical<br />
strength are graphitized carbon black.<br />
A packing material for liquid chromatography is produced by mixing<br />
carbon black, a synthetic resin which can be graphitized, <strong>and</strong> pitches.<br />
Suitable synthetic resins are phenolic resins, furan resins, furfural resins,<br />
divinylbenzene resins, or urea resins. 19 The pitches can be petroleum<br />
pitches, coal-tar pitches, <strong>and</strong> liquefied coal oil. The mixture is granulated<br />
<strong>and</strong> heated up to 3000°C in an inert atmosphere.<br />
7.6.3 Composite Carbon Fiber Materials<br />
Impregnation of carbon fibers <strong>and</strong> subsequent pyrolysis at 1000°C improves<br />
strength of carbon fibers. 20 A yarn is passed through a bath containing<br />
a carbonizable resin precursor, such as a partially polymerized furfuryl<br />
alcohol. It is advantageous to add a latent catalyst along with the precursor.<br />
Suitable catalysts are a complex of boron trifluoride <strong>and</strong> ethylamine or<br />
maleic anhydride.<br />
The use of a latent catalyst allows the application of a low-viscosity<br />
solution to the fiber with subsequent polymerization at the elevated temperatures.<br />
If the precursor were to polymerize significantly prior to application,<br />
the treating bath would be so viscous that would allow only a coating<br />
to be formed.<br />
For high performance composite carbon fiber reinforced carbonaceous<br />
material which is compositely reinforced with carbon fibers, prepregs<br />
of woven fabrics of carbon fibers are impregnated with a resin such as<br />
phenol resin, furan resin, epoxy resin, urea resin, etc. They then are lamin-
316 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
ated as a matrix <strong>and</strong> molded under heat <strong>and</strong> pressure, <strong>and</strong> after carbonization,<br />
they are further graphitized by heating to a temperature of 3000°C. 21<br />
7.6.4 Foundry Binders<br />
Furans are somewhat more expensive than other binders, but the possibility<br />
of s<strong>and</strong> reclamation is advantageous. One of the most commercially<br />
successful no-bake binders is the phenolic-urethane no-bake binder. This<br />
binder provides molds <strong>and</strong> cores with excellent strengths that are produced<br />
in a highly productive manner.<br />
Furan-based binders have less VOC, free phenol level, low formaldehyde,<br />
<strong>and</strong> produce less odor <strong>and</strong> smoke during core making <strong>and</strong> castings.<br />
However, the curing performance of furan binders is much slower than the<br />
curing of phenolic urethane no-bake binders.<br />
Furan binders can be modified to increase their reactivity, for instance<br />
by formulating with urea/formaldehyde resins, phenol/formaldehyde<br />
resins, novolak resins, phenolic resol resins, <strong>and</strong> resorcinol. Nevertheless,<br />
these modified furan binders do not provide the cure speed needed<br />
in foundries that require high productivity. Therefore, an activator, which<br />
promotes the polymerization of furfuryl alcohol, is added. Resorcinol pitch<br />
is used for this purpose. 22 Further components in such a formulation are<br />
polyester polyols or polyether polyols, <strong>and</strong> a silane, such as (3-aminopropyl)triethoxysilane.<br />
The curing process of urea-modified furan resins in s<strong>and</strong>s has been<br />
investigated by infrared spectroscopy. 23<br />
7.6.5 Glass Fiber Binders<br />
An alternative to phenol/formaldehyde-based fiberglass binders is furanbased<br />
binders. Furan binders provide many of the advantages of phenolic<br />
binders while resulting in substantially reduced VOC emissions. Water as<br />
a significant component can be used. Formaldehyde is not a significant<br />
curing or decomposition by-product, <strong>and</strong> the furan resins form very rigid<br />
thermosets.<br />
Emulsified furan resins can be used. Emulsified furan-based glass<br />
fiber binding compositions are advantageous since they allow the use of<br />
furan resins that have high molecular weights or the addition of other materials<br />
which would give rise to the formation of two-phase systems. 6 A<br />
suitable surfactant to be added to the furan binder compositions is sodium
Furan Resins 317<br />
dodecyl benzene sulfonate. It may be added in an amount from 0.05 to<br />
1.0%.<br />
7.6.6 Oil Field <strong>Applications</strong><br />
Wells in s<strong>and</strong>y, oil-bearing formations are frequently difficult to operate<br />
because the s<strong>and</strong> in the formation is poorly consolidated <strong>and</strong> tends to flow<br />
into the well with the oil. S<strong>and</strong> production is a serious problem because the<br />
s<strong>and</strong> causes erosion <strong>and</strong> premature wearing out of the pumping equipment.<br />
It is a nuisance to remove from the oil at a later point in the operation.<br />
Furan resin formulations can be used for in-situ chemical s<strong>and</strong> consolidation.<br />
24<br />
7.6.7 Plant Growth Substrates<br />
Conventional mineral wool plant growth substrates are based on a coherent<br />
matrix of mineral wool of which the fibers are mutually connected by a<br />
cured binder.<br />
There is a need to reduce the phytotoxicity of the chemicals used.<br />
The phytotoxicity may result from the phenolic binder materials. If a phenolic<br />
resin is used as binder, a wetting agent must be added in order to impart<br />
the hydrophobic mineral wool matrix with hydrophilic properties. However,<br />
the use of a furan resin allows the ab<strong>and</strong>onment of the use of a wetting<br />
agent.<br />
A disadvantage of the use of a furan resin is its comparatively high<br />
price. Therefore, the traditional phenol/formaldehyde resin substituted<br />
only partly by a furan resin, is sufficient to maintain or to achieve the desired<br />
properties.<br />
25, 26<br />
7.6.8 Photosensitive Polymer Electrolytes<br />
Both conjugated furan chromophores <strong>and</strong> polyethers can be grafted onto<br />
chitosan to result in a photosensitive polymer electrolyte. The furan chromophore<br />
consists of conjugated furan chromophores of 5-[2-(5-Methyl furylene<br />
vinylene)]furancarboxyaldehyde, 27 c.f. Figure 7.5. The graft polymer<br />
can be photocrosslinked. The photochemical reaction consists of a π 2 +π 2<br />
cycloaddition reaction of the vinylene double bonds of the furan moiety so<br />
that two pendent vinylene groups form a four membered ring. The crosslinking<br />
reaction is shown in Figure 7.6
318 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
H 3 C<br />
O<br />
O<br />
O<br />
C<br />
H<br />
Figure 7.5: 5-[2-(5-Methyl furylene vinylene)]furancarboxyaldehyde<br />
OH<br />
OH<br />
O<br />
O<br />
O<br />
O<br />
NH<br />
CH 2<br />
O<br />
CH 3<br />
O<br />
NH<br />
CH 2<br />
O<br />
CH 3<br />
O<br />
O<br />
CH 3<br />
O<br />
O<br />
O<br />
CH 3<br />
CH 2<br />
NH<br />
CH 2<br />
NH<br />
O<br />
O<br />
O<br />
O<br />
OH<br />
OH<br />
Figure 7.6: Photo Crosslinking of the Furylene Vinylene Units Grafted on Chitosan
Furan Resins 319<br />
REFERENCES<br />
1. Z. László-Hedvig <strong>and</strong> M. Szesztay. Furan resins (2-furfuryl alcohol based).<br />
In J. C. Salamone, editor, The Polymeric Materials Encyclopaedia: Synthesis,<br />
Properties <strong>and</strong> <strong>Applications</strong>, pages 548–549. CRC Press, Boca Raton, FL,<br />
1999.<br />
2. A. G<strong>and</strong>ini <strong>and</strong> M. N. Belgacem. Furans in polymer chemistry. Prog. Polym.<br />
Sci., 22(6):1203–1379, 1997.<br />
3. I. F. C. B.V. Historical overview <strong>and</strong> industrial development. (Internet:<br />
http://www.furan.com).<br />
4. C. Claessen. Process for the treatment of wood or other substances containing<br />
cellulose for the purpose of obtaining cellulose <strong>and</strong> artificial resin, asphalt,<br />
lac <strong>and</strong> the like. GB Patent 160 482, March 17 1921.<br />
5. J. S. Stokes. Improvements in <strong>and</strong> relating to synthetic resin composition.<br />
GB Patent 243 470, December 3 1925.<br />
6. T. J. Taylor, W. H. Kielmeyer, C. M. Golino, <strong>and</strong> C. A. Rude. Emulsified<br />
furan resin based glass fiber binding compositions, process of binding<br />
glass fibers, <strong>and</strong> glass fiber compositions. US Patent 6 077 883, assigned to<br />
Johns Manville International, Inc. (Denver, CO); QO Chemicals, Inc. (West<br />
Lafayette, IN), June 20 2000.<br />
7. E. Goiti, F. Heatley, M. B. Huglin, <strong>and</strong> J. M. Rego. Kinetic aspects of the<br />
Diels-Alder reaction between poly(styrene-co-furfuryl methacrylate) <strong>and</strong> bismaleimide.<br />
Eur. Polym. J., 40(7):1451–1460, July 2004.<br />
8. C. Moreau, M. N. Belgacem, <strong>and</strong> A. G<strong>and</strong>ini. Recent catalytic advances in<br />
the chemistry of substituted furans from carbohydrates <strong>and</strong> in the ensuing<br />
polymers. Top. Catal., 27(1-4):11–30, February 2004.<br />
9. K. S. Patel, K. R. Desai, K. H. Chikhalia, <strong>and</strong> H. S. Patel. Polyimides based<br />
on poly(2-furanmethanol-formaldehyde). Adv. Polym. Technol., 23(1):76–80,<br />
2004.<br />
10. K. Kawamura <strong>and</strong> S. Ozawa. Characterization of fiber reinforced plastics<br />
made from aramid <strong>and</strong> phenol resin or furan resin. Kobunshi Ronbunshu,<br />
59(1):51–56, 2002.<br />
11. R. Gubler, editor. Chemical Economics H<strong>and</strong>book (CEH). SRI Consulting, a<br />
Division of Access Intelligence, Menlo Park, CA, 1950–to present. (Internet:<br />
http://ceh.sric.sri.com/).<br />
12. S. Bizzari. Report “Formaldehyde”. In Chemical Economics H<strong>and</strong>book<br />
(CEH). SRI Consulting, a Division of Access Intelligence, Menlo Park, CA,<br />
January 2004. (Internet: http://ceh.sric.sri.com/).<br />
13. J. Levy <strong>and</strong> Y. Sakuma. Report “Furfural”. In Chemical Economics H<strong>and</strong>book<br />
(CEH). SRI Consulting, a Division of Access Intelligence, Menlo Park,<br />
CA, July 2001. (Internet: http://ceh.sric.sri.com/).
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14. N. Meyer <strong>and</strong> M. Cousin. Furan resins of improved fire resistance. US<br />
Patent 4 355 145, assigned to Societe Chimique des Charbonnages SA (Paris<br />
La Defense, FR), October 19 1982.<br />
15. K. Hoshi, T. Akatsu, Y. Tanabe, <strong>and</strong> E. Yasuda. Curing properties of furfuryl<br />
alcohol condensate with carbonaceous fine particles under ultrasonication.<br />
Ultrason. Sonochem., 8(2):89–92, April 2001.<br />
16. C. Gousse, A. G<strong>and</strong>ini, <strong>and</strong> P. Hodge. Application of the Diels-Alder reaction<br />
to polymers bearing furan moieties. 2. Diels-Alder <strong>and</strong> retro-Diels-Alder reactions<br />
involving furan rings in some styrene copolymers. Macromolecules,<br />
31(2):314–321, January 1998.<br />
17. K. Fukuyama, T. Nishizawa, <strong>and</strong> K. Nishikawa. Investigation of the pore<br />
structure in glass-like carbon prepared from furan resin. Carbon, 39(13):<br />
2017–2021, November 2001.<br />
18. Y. Korai, K. Sakamoto, I. Mochida, <strong>and</strong> O. Hirai. Structural correlation between<br />
micro-texture of furan resin <strong>and</strong> its derived glass-like carbon. Carbon,<br />
42(1):221–223, 2004.<br />
19. H. Ichikawa, A. Yokoyama, T. Kawai, H. Moriyama, K. Komiya, <strong>and</strong> Y. Kato.<br />
Packing material for liquid chromatography <strong>and</strong> method of manufacturing<br />
thereof. US Patent 5 270 280, assigned to Nippon Carbon Co., Ltd. (Tokyo,<br />
JP); Tosoh Corporation (Yamaguchi, JP), December 14 1993.<br />
20. M. Katz. Improvement of carbon fiber strength. EP Patent 0 251 596, assigned<br />
to Du Pont, January 7 1988.<br />
21. T. Kawakubo <strong>and</strong> E. Oota. Process for preparation of carbon fiber composite<br />
reinforced carbonaceous material. US Patent 5 096 519, assigned to<br />
Mitsubishi Pencil Co., Ltd. (JP), March 17 1992.<br />
22. K. K. Chang. Furan no-bake foundry binders <strong>and</strong> their use. US Patent<br />
6 593 397, assigned to Ashl<strong>and</strong> Inc. (Dublin, OH), July 15 2003.<br />
23. M. Bilska <strong>and</strong> M. Holtzer. Application of fourier transform infrared spectroscopy<br />
(FTIR) to investigation of moulding s<strong>and</strong>s with furan resins hardening<br />
process. Arch. Metall., 48(2):233–242, 2003.<br />
24. P. Shu. Water compatible chemical in situ <strong>and</strong> s<strong>and</strong> consolidation with furan<br />
resin. US Patent 5 522 460, assigned to Mobil Oil Corporation (Fairfax, VA),<br />
June 4 1996.<br />
25. E. L. Hansen <strong>and</strong> J. F. De Groot. Process for the manufacture of a mineral<br />
wool plant growth substrate. US Patent 6 562 267, assigned to Rockwool<br />
International A/S (Hedenhusene, DK), March 13 2003.<br />
26. J. F. De Groot <strong>and</strong> T. B. Husemoen. Hydrophilic plant growth substrate,<br />
comprising a furan resin. US Patent 6 032 413, assigned to Rockwool International<br />
A/S (DK), March 7 2000.<br />
27. A. G<strong>and</strong>ini, S. Hariri, <strong>and</strong> J.-F. Le Nest. Furan-polyether-modified chitosans<br />
as photosensitive polymer electrolytes. Polymer, 44(25):7565–7572, December<br />
2003.
8<br />
Silicones<br />
In contrast to most organic polymers, in silicones the backbone is made of<br />
silicon <strong>and</strong> oxygen. Silicon is together with carbon in the fourth group of<br />
the periodic system, therefore a similar behavior of these elements can be<br />
expected.<br />
8.1 HISTORY<br />
Kipping ∗ started with the synthesis of organic silicon compounds by treating<br />
SiCl 4 with magnesium-based organometallic compounds. These compounds<br />
are now called Grignard reagents, invented by Victor Grignard in<br />
1900.<br />
Hyde † , at Corning, developed a flexible, high temperature binder for<br />
glass fibers <strong>and</strong> synthesized the first silicone polymer. The potential applications<br />
in other fields, such as electric industries soon became apparent.<br />
Eugene George Rochow ‡ at General Electric developed synthesis of<br />
silicones that is now used. 1, 2 His first patent dates at 1941. 3, 4<br />
In 1949,the silly putty was invented by James Wright when mixing<br />
silicone oil with boric acid. Silly putty acts like both a rubber <strong>and</strong> a putty.<br />
∗ Frederic Stanley Kipping, born in Upper Broughton (UK) 1863, died in 1949<br />
† James Franklin Hyde, born in Solvay, New York 1903, died in 1999<br />
‡ Eugene George Rochow, born in Newark, New Jersey 1909, died in 2002<br />
321
322 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
8.2 MONOMERS<br />
8.2.1 Chlorosilanes<br />
The synthesis of silanes <strong>and</strong> siloxanes starts from chlorosilanes such as dimethyldichlorosilane.<br />
Other products are derived from this compound that<br />
also serve as monomers. Thus, in silicone chemistry, the term monomer is<br />
not as clearly defined as in other fields of polymer chemistry.<br />
8.2.2 Silsesquioxanes<br />
Silsesquioxane resins are used in industrial applications in the automotive,<br />
aerospace, naval, <strong>and</strong> other manufacturing industries. Silsequioxane resins<br />
exhibit excellent heat <strong>and</strong> fire resistant properties that are desirable for such<br />
applications. These properties make the silsesquioxane resins attractive for<br />
use in fiber-reinforced composites for electrical laminates, <strong>and</strong> structural<br />
use in automotive components, aircraft, <strong>and</strong> naval vessels.<br />
There is a need for rigid silsesquioxane resins that has increased<br />
flexural strength, flexural strain, fracture toughness, <strong>and</strong> fracture energy,<br />
without significant loss of modulus or loss of thermal stability. In addition,<br />
rigid silsesquioxane resins have low dielectric constants <strong>and</strong> are useful<br />
as interlayer dielectric materials. Rigid silsesquioxane resins are also<br />
useful as abrasion resistant coatings. These applications require that the<br />
silsesquioxane resins exhibit high strength <strong>and</strong> toughness. 5<br />
The formation of silsesquioxanes is shown in Figure 8.1. Silsesquioxanes<br />
are organosilicon compounds with the formula [RSiO 3/2 ] n .<br />
[R 7 Si 7 O 9 (OH) 3 ], as shown in Figure 8.1, can be synthesized in one<br />
step via the hydrolytic condensation of RSiCl 3 or RSi(OMe) 3 . A single<br />
Si-O-Si linkage in a fully condensed R 8 Si 8 O 12 framework can be cleaved<br />
selectively by strong acids (e.g., HBF 4 /BF 3 or triflic acid. 6<br />
8.2.3 Hydrogen Silsesquioxanes<br />
Hydrogen-silsesquioxane resins are useful precursor substances for silicacontaining<br />
ceramic coatings. Hydrogen silsesquioxane resins are ladder or<br />
cage polymers. 7 The general structure is shown in Figure 8.2. When trichlorosilane<br />
is subjected to hydrolytic condensation caused by direct contact<br />
with water, the reaction occurs abruptly, <strong>and</strong> gels are formed. Accordingly,<br />
various methods for manufacturing hydrogen-silsesquioxane resins
Silicones 323<br />
R<br />
Si<br />
OH<br />
R<br />
Cl<br />
Si<br />
Cl<br />
Cl<br />
H 2 O<br />
O<br />
R<br />
O<br />
Si<br />
O<br />
Si<br />
O<br />
O<br />
Si<br />
R<br />
R O<br />
OH<br />
R<br />
O<br />
Si OH<br />
Si<br />
R<br />
O<br />
O<br />
Si<br />
R<br />
Figure 8.1: Formation of Silsesquioxanes: [R 7 Si 7 O 9 (OH) 3 ]<br />
H<br />
HO<br />
Si<br />
O<br />
Si<br />
HO<br />
H<br />
H H<br />
O<br />
Si<br />
O Si<br />
O O<br />
O Si O<br />
Si<br />
H H<br />
H H<br />
O Si<br />
O Si<br />
O O<br />
O<br />
Si<br />
O<br />
H<br />
n<br />
Si<br />
H<br />
OH<br />
OH<br />
H<br />
Si<br />
O<br />
O<br />
O<br />
O<br />
H<br />
Si<br />
O<br />
H<br />
Si Si<br />
H<br />
O<br />
O<br />
O<br />
O<br />
O<br />
H<br />
Si<br />
O<br />
Si<br />
H<br />
H<br />
Si<br />
O<br />
Si<br />
H<br />
Figure 8.2: Hydrogen silsesquioxane resins. 7 Top: Ladder Form, Bottom: Cage<br />
Form
324 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
that do not form gels have been proposed. The hydrogen-silsesquioxane<br />
resin can be manufactured in an aromatic hydrocarbon solution of trichlorosilane.<br />
The hydrolytic condensation is then performed as a two-phase<br />
reaction with concentrated sulfuric acid.<br />
Concentrated sulfuric acid <strong>and</strong> aromatic hydrocarbon react to produce<br />
an arylsulfonic acid hydrate, <strong>and</strong> the water in this hydrate contributes<br />
to the hydrolytic condensation of trichlorosilane. Therefore, the hydrogensilsesquioxane<br />
resin produced by this hydrolytic condensation is obtained<br />
from the organic phase.<br />
When water is added to the concentrated sulfuric acid phase in order<br />
to recover <strong>and</strong> reuse the arylsulfonic acid, precipitation occurs, thus<br />
rendering the arylsulfonic acid unsuitable for reuse. For this reason, large<br />
quantities of organic solvent <strong>and</strong> sulfuric acid are lost using this method.<br />
A method for complete reuse of the solvent, the sulfuric acid <strong>and</strong> surfactants,<br />
essentially without loss of these compounds, has been described. The<br />
method utilizes a two-phase system consisting of an aqueous phase:<br />
1. An aqueous solution consisting of sulfuric acid <strong>and</strong> an organic<br />
sulfonic acid, e.g., p-toluenesulfonic acid monohydrate, <strong>and</strong><br />
2. The organic phase consisting of a diluted solution of organic sulfonic<br />
acid in a halogenated hydrocarbon solvent. The trichlorosilane<br />
must be soluble in this solvent, <strong>and</strong> the solvent should not react<br />
with sulfuric acid. Examples are isopropyl chloride, chlorobenzene,<br />
<strong>and</strong> others.<br />
This method results in hydrogen-silsesquioxane resins at a high yield.<br />
The loss of the organic solvent used in the organic phase is small, <strong>and</strong> the<br />
precipitation of benzenesulfonic acid, etc., in the aqueous phase due to supersaturation<br />
can also be eliminated. The organic solvent, the sulfuric acid<br />
<strong>and</strong> the organic sulfonic acid used in the aqueous phase can be effectively<br />
reused. 8<br />
8.2.4 Alkoxy Siloxanes<br />
Examples of alkoxy siloxanes are listed in Table 8.1. Trifunctional siloxane<br />
units <strong>and</strong> tetrafunctional siloxane units are used to improve the physical<br />
properties of curable epoxy resins. Branched silicone resins with trifunctional<br />
siloxane units are highly heat-resistant <strong>and</strong> have an excellent capacity<br />
for film-formation, which is why they are used as electrical insulating
Table 8.1: Epoxy-containing Siloxanes 9<br />
Siloxane<br />
Methyltrimethoxysilane<br />
Methyltriethoxysilane<br />
Ethyltrimethoxysilane<br />
Ethyltriethoxysilane<br />
Vinyltrimethoxysilane<br />
Phenyltrimethoxysilane<br />
3,3,3-Trifluoropropyltrimethoxysilane<br />
Dimethyldimethoxysilane<br />
Methylphenyldimethoxysilane<br />
Methylvinyldimethoxysilane<br />
Diphenyldimethoxysilane<br />
Dimethyldiethoxysilane<br />
Methylphenyldiethoxysilane<br />
Tetramethoxysilane<br />
Tetraethoxysilane (TEOS)<br />
Tetrapropoxysilane<br />
Dimethoxydiethoxysilane<br />
Silicones 325<br />
materials, <strong>and</strong> heat-resistant paints <strong>and</strong> coatings. 9<br />
8.2.5 Epoxy-modified Siloxanes<br />
Siloxanes with pendent epoxy groups are listed in Table 8.2. Epoxy-containing<br />
silicone resins are prepared either by the co-hydrolysis <strong>and</strong> condensation<br />
of epoxy-containing trialkoxysilane <strong>and</strong> diorganodialkoxysilane or<br />
by the base-catalyzed equilibration polymerization of cyclic diorganosiloxane<br />
<strong>and</strong> epoxy-containing trialkoxysilane. 9 Epoxy-containing silicone<br />
resins have broad molecular weight distributions <strong>and</strong> do not exhibit a softening<br />
point or a distinct glass transition temperature.<br />
8.2.6 Silaferrocenophanes<br />
Silaferrocenophanes are of considerable interest because they may serve<br />
as precursors to unusual ceramic materials. <strong>Polymers</strong> can be made by<br />
ring opening polymerization as shown in Figure 8.3. Other ferrocenophanes<br />
bridged by heteroatoms such as germanium <strong>and</strong> phosphorus have<br />
been synthesized. In the presence of methylphenylchlorosilane or diphenylchlorosilane,<br />
i.e., silanes with pendent hydrogen, telechelic polymers can
326 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Siloxane<br />
Table 8.2: Epoxy-containing Siloxanes 9<br />
3-Glycidoxypropyl(methyl)dimethoxysilane<br />
3-Glycidoxypropyl(methyl)diethoxysilane<br />
3-Glycidoxypropyl(methyl)dibutoxysilane<br />
2-(3,4-Epoxycyclohexyl)ethyl(methyl)dimethoxysilane<br />
2-(3,4-Epoxycyclohexyl)ethyl(phenyl)diethoxysilane<br />
2,3-Epoxypropyl(methyl)dimethoxysilane<br />
2,3-Epoxypropyl(phenyl)dimethoxysilane<br />
3-Glycidoxypropyltrimethoxysilane (GLYMO)<br />
3-Glycidoxypropyltriethoxysilane<br />
3-Glycidoxypropyltributoxysilane<br />
2-(3,4-Epoxycyclohexyl)ethyltrimethoxysilane<br />
2-(3,4-Epoxycyclohexyl)ethyltriethoxysilane<br />
2,3-Epoxypropyltrimethoxysilane<br />
2,3-Epoxypropyltriethoxysilane<br />
Fe<br />
CH 3<br />
Si<br />
CH 3<br />
Fe<br />
CH 3<br />
Si<br />
CH 3<br />
Figure 8.3: Ring Opening Polymerization of Silaferrocenophanes
Silicones 327<br />
Table 8.3: Products Obtained by the Rochow Synthesis 10<br />
Silane Yields [%] Boiling Points [°C]<br />
Methyldichlorosilane 0.5 41<br />
Methyltrichlorosilane 8–18 66<br />
Dimethyldichlorosilane 80–85 70<br />
Trimethylchlorosilane 2–4 57<br />
be produced with the hydrogen bearing silanes as end group 11, 12 Apart<br />
from silaferrocenophanes, ferrocenophanes with conjugated double bonds<br />
instead of silicon are of interest because of their electrical properties. 13<br />
8.2.7 Synthesis<br />
8.2.7.1 Direct Synthesis<br />
Silicones are synthesized via methylchlorosilanes by the Müller-Rochow<br />
process. The reaction is carried out at temperatures of 250 to 300°C <strong>and</strong><br />
2 to 5 bars. A copper catalyst used with antimony, cadmium, aluminum,<br />
zinc, <strong>and</strong> tin is effective for improving the activity. However, lead would<br />
act as an inhibitor.<br />
A finely homogenized mixture of silicon <strong>and</strong> copper is introduced<br />
into a fluidized bed reactor. The reactor is fluidized by gaseous methylchloride.<br />
The reactants are separated from the solid components <strong>and</strong> on<br />
cooling a crude liquid silane mixture is obtained. Silicon conversions of<br />
90 to 98% <strong>and</strong> methylchloride conversions of 30 to 90% can be achieved.<br />
The reaction is strongly exothermic <strong>and</strong> requires a precise control. Dimethyldichlorosilane<br />
is the main product. Other major products obtained are<br />
shown in Table 8.3. The selectivity for producing dimethyldichlorosilane<br />
is highly sensitive to trace amounts of other metals present. The selectivity<br />
for dimethyldichlorosilane is reduced if the Cu, Zn, or Sn concentrations<br />
exceed the generally used concentrations or if the reaction temperature<br />
exceeds 300°C. A silver promoter increases the selectivity to dimethyldichlorosilane.<br />
14, 15 The crude silane mixture is then separated in distillation<br />
columns. A high separating capacity is needed, because the boiling<br />
points of CH 3 SiCl 3 <strong>and</strong> (CH 3 ) 2 SiCl 2 differ by only 4°C. A high purity is<br />
required, because even a small amount of CH 3 SiCl 3 leads to branched <strong>and</strong><br />
eventually gelled products.
328 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
8.2.7.2 Hydrosilylation<br />
The hydrosilylation reaction consists of the addition of hydrogen-containing<br />
silanes to products with double or triple bonds. This reaction is suitable<br />
for introducing organo functions into silicone compounds. Therefore, hydrosilylation<br />
is extensively used to synthesize organofunctional silicones<br />
with pendant vinyl groups, amino groups, etc. 16 In a further step, chlorine<br />
atoms, hydrogen atoms, <strong>and</strong> alkoxy groups can undergo a nucleophilic<br />
substitution. The hydrosilylation reaction requires often high temperatures.<br />
Vinyl Groups. The hydrosilylation of aromatic compounds containing<br />
vinyl unsaturation can lead to radical polymerization of the monovinylaromatic<br />
compounds, especially at elevated temperature. The use of radical<br />
polymerization inhibitors, such as phenols or quinones, is often necessary,<br />
however, most of these inhibitors are not sufficiently active at elevated<br />
temperatures <strong>and</strong> require the presence of oxygen to improve their activity.<br />
However, special conditions <strong>and</strong> precautions make the use of a radical<br />
polymerization inhibitor unnecessary. Styrene <strong>and</strong> α-methylstyrene can be<br />
hydrosilylated with heptamethyltrisiloxane with a Karstedt platinum catalyst<br />
at 90°C. 17<br />
When 4-vinyl-1-cyclohexene is reacted with a hydrogenchlorosilane,<br />
both the vinylic double bond <strong>and</strong> the double bond in the cyclohexene<br />
ring react. Thereby an organic silicon compound of the formula given in<br />
Figure 8.4 is obtained in which the hydrogenchlorosilane is added to each<br />
of the two double bonds in 4-vinyl-1-cyclohexene. The cyclohexane ring<br />
within the molecule imparts a high hardness <strong>and</strong> scratch resistance <strong>and</strong> is<br />
useful as a coupling agent to be added to paints for use in automobiles,<br />
buildings <strong>and</strong> adhesives. The compound is also useful as an intermediate<br />
to an alkoxysilane coupling agent. 18<br />
8.2.7.3 Grignard Synthesis<br />
The Grignard synthesis is suitable to introduce organic groups to silicon.<br />
The Grignard synthesis is used on a laboratory scale. An example for a<br />
Grignard synthesis is shown in Figure 8.5. With water, methylphenyldichlorosilane<br />
condenses to a linear polymer.
Silicones 329<br />
H<br />
CH 3<br />
Si Cl<br />
+ + H<br />
CH 3<br />
Si Cl<br />
Cl<br />
Cl<br />
CH 3<br />
CH 3<br />
Si Cl<br />
Cl<br />
Si<br />
Cl<br />
Cl<br />
+<br />
CH 3<br />
Cl<br />
Si<br />
CH 3<br />
Si Cl<br />
Cl<br />
Cl<br />
Figure 8.4: Hydrosilylation of 4-Vinyl-1-cyclohexene<br />
Cl<br />
Cl<br />
Mg Br + Cl Si Cl<br />
Si Cl + MgClBr<br />
Cl<br />
Cl<br />
Cl<br />
CH 3<br />
CH 2<br />
Mg<br />
Br + Cl<br />
Si<br />
Cl<br />
Cl<br />
CH 3<br />
CH 2<br />
Si<br />
+ MgClBr<br />
Cl<br />
Figure 8.5: Grignard Synthesis
330 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
8.2.7.4 Condensation<br />
Hydrolysis of chlorosilanes results in silanols. These silanols are not stable<br />
<strong>and</strong> undergo a polycondensation. Intramolecular <strong>and</strong> intermolecular condensation<br />
takes place. Intermolecular condensation yields linear siloxanes,<br />
<strong>and</strong> intramolecular condensation yields cyclic products. When trichlorosilanes<br />
undergo hydrolysis, highly crosslinked silicone resins are obtained.<br />
The reaction can be catalyzed by acids. An equilibrium between the linear<br />
siloxanes <strong>and</strong> cyclic siloxanes can be established.<br />
If the catalyst is deactivated, the condensation stops <strong>and</strong> the cyclic<br />
products that consist mostly of a tetramer can be removed by distillation.<br />
On the other h<strong>and</strong>, cyclic siloxanes can be transformed to polymers in the<br />
presence of alkali. If the catalyst is not deactivated then cyclic siloxane<br />
forms until the equilibrium is established. In equilibrium ca. 20% of cyclic<br />
products are present, which is relevant to the recycling of polysiloxanes.<br />
Chain Stoppers. To obtain stable or functional terminal groups, chain<br />
stoppers are added. The reaction proceeds under continuous cleavage <strong>and</strong><br />
recombination of siloxane bonds. The reaction is catalyzed by acids.<br />
Bodying. Bodying is a technology that consists of the base-catalyzed<br />
depletion of the silanol groups in a silicone resin prepared by the hydrolysis<br />
<strong>and</strong> condensation of organoalkoxysilane. In this process the molecular<br />
weight of the silicone resin is simply increased, while control of the<br />
molecular weight, softening point, <strong>and</strong> glass transition temperature is not<br />
possible. 9<br />
Crosslinking. The degree of crosslinking depends on the presence of<br />
either tetrachlorosilane SiCl 4 for the production of very rigid resins, or<br />
(CH 3 ) 2 SiCl 2 for softer grades.<br />
8.2.8 Manufacture<br />
Commercially produced silicone resins comprise:<br />
• Non-meltable solids<br />
• Soluble reactive resins<br />
• Silsesquioxanes<br />
• High reactive alkoxysiloxanes with molecular weight.
Silicones 331<br />
8.3 MODIFIED TYPES<br />
8.3.1 Chemical Modifications<br />
<strong>Reactive</strong> alkoxysiloxanes can undergo a reaction with functional organic<br />
resins. The modification of methylpolysiloxanes is achieved by substituting<br />
the methyl groups with other organic groups, e.g., lower alkyl chains or<br />
functional groups like vinyl groups, or by copolymerization with organic<br />
polymers, e.g., poly(ethylene oxide) or poly(propylene oxide).<br />
8.3.1.1 Amine Functions<br />
Aminofunctional silicones impart extreme softness. Such materials are appreciated<br />
in textiles because of the improved wear comfort. In textile dyeing<br />
uniformity of color fixation is achieved by efficient control of foaming<br />
in the dyeing bath.<br />
8.3.1.2 Functionalized Silanes<br />
<strong>Reactive</strong> silanes or siloxanes can also include functionalities such as: vinyl,<br />
hydride, allyl, or other unsaturated groups. For surface coating, hexamethyldisiloxane<br />
<strong>and</strong> tetramethyldivinyldisiloxane are used. 5 Mixtures of<br />
siloxanes with trimethyl silyl groups <strong>and</strong> dimethylvinyl silyl groups are<br />
also common.<br />
8.3.1.3 Crosslinking Agents<br />
Crosslinking agents include alkoxysilanes such as methyltrimethoxysilane,<br />
dimethyldimethoxysilane, etc., or oxime silanes, for example, methyltris-<br />
(methylethylketoxime)silane. 19 Crosslinking accelerators include amines,<br />
tin compounds such as dibutyltin diacetate, or dibutyltin dilaurate. 19<br />
8.3.2 Fillers<br />
The silicone network does not exhibit much mechanical strength. Mechanical<br />
strength is imparted by the interaction of a filler with the polymer.<br />
Fumed silica shows the strongest reinforcing effect. Other fillers include<br />
quartz flour, iron oxide, <strong>and</strong> carbon black.
332 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
8.3.3 Reinforcing Materials<br />
Fiber reinforced, silicone matrix resin composites find many applications<br />
in structural components. Fiber reinforcement often takes the form of woven<br />
glass fiber mats. Woven carbon fiber mats offer a higher modulus<br />
reinforcing media, but they are more expensive than glass fibers. Other<br />
fiber compositions such as aramid, nylon, polyester, <strong>and</strong> quartz fibers may<br />
be used for reinforcement. Other fibrous forms, such as non-woven mats<br />
<strong>and</strong> layers of loose fibers, may also be used in silicone-based composite<br />
applications. 20<br />
Fiber reinforced, silicone matrix resin composites in multilayer laminated<br />
form are strong <strong>and</strong> fire resistant. They find applications in interiors<br />
of airplanes <strong>and</strong> ships. They are also used in electrical applications, such<br />
as wiring boards <strong>and</strong> printed circuit boards, requiring flexural strength <strong>and</strong><br />
low weight.<br />
Suitable resin types are typically highly branched <strong>and</strong> crosslinked<br />
polymer molecules, when cured. To facilitate the impregnation process,<br />
silicone precursor formulations may be diluted with toluene. The toluene<br />
is then evaporated from the composite.<br />
8.4 CURING<br />
8.4.1 Curing by Condensation<br />
Curing by condensation releases alcohol, amines, acetic acid, or other<br />
volatile reaction products.<br />
The polymerization reaction does proceed in the absence of water.<br />
This fact is utilized in one component systems that form polymers<br />
by means of atmospheric humidity. To avoid premature curing, the components<br />
are packed in compartments that are free of moisture <strong>and</strong> tight to<br />
permeation of moisture.<br />
Methoxysilanes can condense with chlorosilanes releasing methylchloride,<br />
21 as shown in Figure 8.6. The reaction is catalyzed by ferric<br />
chloride.<br />
8.4.1.1 Platinum Complexes for Hydrosylilation<br />
Additional crosslinking occurs by reaction of compounds with pendant<br />
vinyl groups. Certain platinum complexes catalyze the hydrosylilation re-
Silicones 333<br />
CH 3<br />
CH 3<br />
Si O CH 3<br />
+ Cl Si O<br />
CH 3 CH 3<br />
CH 3<br />
Si O<br />
CH 3<br />
CH 3<br />
Si O<br />
CH 3<br />
CH 3 Cl<br />
Figure 8.6: Condensation of Methoxysilanes with Chlorosilanes<br />
action.<br />
Suitable platinum catalysts are chloroplatinic acid, dichlorobis(triphenylphosphine)platinum(II),<br />
platinum chloride, platinum oxide, <strong>and</strong> also<br />
complexes of platinum compounds. For example, a Karstedt catalyst is a<br />
complex of chloroplatinic acid with 1,3-divinyl-1,1,3,3-tetramethyldisiloxane<br />
<strong>and</strong> 1,3-diethenyl-1,1,3,3-tetramethyldisiloxane. 5<br />
Synergistic catalyst systems are mixtures of the compounds H 2 PtCl 6<br />
<strong>and</strong> RuCl 3 × nH 2 O. 22 The hydrosilylation reaction proceeds at room temperature.<br />
However, using inhibitors the temperature can be increased.<br />
8.4.1.2 Hydrosilylation Inhibitors<br />
Hydrosilylation inhibitors fall into two general classes. 23 One class is composed<br />
of materials that effectively inhibit hydrosilylation over a wide range<br />
of temperatures <strong>and</strong> can be volatilized out of the organosilicon composition<br />
to allow hydrosilylation to proceed. Examples of this class are pyridine,<br />
acrylonitrile, 2-ethenylisopropanol, <strong>and</strong> perchloroethylene.<br />
The other class of inhibitors is materials that are non-volatile. The<br />
inhibitory effect of these materials is overcome by heating, whereupon<br />
hydrosilylation takes place. Examples of this latter class are the reaction<br />
product of a siloxane having silicon-bonded hydrogen atoms, a platinum<br />
catalyst, <strong>and</strong> an acetylenic alcohol, organic phosphines <strong>and</strong> phosphites,<br />
benzotriazole, organic sulfoxides, metallic salts, aminofunctional<br />
siloxanes, ethylenically unsaturated isocyanurates olefinic siloxanes, dialkyl<br />
carboxylic esters, <strong>and</strong> unsaturated amides. Examples of inhibitors<br />
are shown in Table 8.4.<br />
In polyethers, oxidation impurities inhibit the hydrosilylation of the<br />
polyethers, however, the exact identities of these inhibitors are unknown.<br />
They are believed to include acetal hydroperoxides, allyl hydroperoxides<br />
<strong>and</strong> free radicals localized at the tertiary carbon atoms in the hydrophobic
334 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 8.4: Inhibitors for Platinum Catalysts<br />
Inhibitor<br />
Remarks<br />
Methylbutynol<br />
Ethynyl cyclohexanol Most preferred 5<br />
Diphenylphosphine<br />
3-Methyl-1-dodecyn-3-ol Release coatings 24<br />
3,7,11-Trimethyl-1-dodecyn-3-ol<br />
segments (e.g., propylene oxide) of unsaturated polyethers. Oxidation impurities<br />
are most likely to occur in polyethers which have been stored for a<br />
long period with no or insufficient quantities of antioxidant. However, they<br />
may also be present in freshly prepared polyethers which may have gotten<br />
too hot in the presence of air or oxygen. Polyethers can be stabilized with<br />
mixtures of ascorbic acid <strong>and</strong> sodium ascorbate <strong>and</strong> allyl polyethers. 25<br />
8.4.1.3 Salts<br />
A commercially available curing catalyst material comprises zinc octoate<br />
<strong>and</strong> choline octoate. 20<br />
8.4.1.4 Polymethylsilazanes<br />
Polymethylsilazanes are synthesized by the reaction of ammonia with dimethyldichlorosilane<br />
<strong>and</strong> methyltrichlorosilane. They are effective room<br />
temperature curing agents for silicone resins. However, ammonia is released<br />
in the course of curing. 26<br />
8.5 CROSSLINKING<br />
Crosslinking can be achieved by different reactions at high temperatures<br />
for HTV-rubber <strong>and</strong> at room temperature for RTV-rubber. The liquid RTVsilicone<br />
rubber can crosslink both by condensation <strong>and</strong> by addition mechanisms.<br />
8.5.1 Condensation Crosslinking<br />
Condensation crosslinking occurs between α,ω-dihydroxypoly(dimethylsiloxane)s<br />
<strong>and</strong> silicates in the presence of inorganic compounds. The cross-
Silicones 335<br />
linking density depends on the functionality <strong>and</strong> concentration of the crosslinking<br />
agent <strong>and</strong> the nature of the catalyst.<br />
8.5.2 Peroxides<br />
Crosslinking at higher temperatures in the range 100 to 160°C is achieved<br />
by the addition of peroxides. Suitable formulations contain a small amount<br />
of vinyl groups.<br />
8.5.3 Hydrosilylation Crosslinking<br />
The hydrosilylation reaction is suitable for final crosslinking or curing reactions.<br />
8.5.3.1 Thermoplastic Elastomers<br />
Hydrosilylation crosslinking can be used to prepare a thermoplastic elastomer.<br />
A thermoplastic elastomer is a polymer or polymeric blend that can<br />
be processed <strong>and</strong> recycled in the same way as a conventional thermoplastic<br />
material. However, it has some properties <strong>and</strong> functional performance<br />
similar to those of vulcanized rubber at the service temperature.<br />
Elastomeric rubber blends are used in the production of high performance<br />
thermoplastic elastomers, particularly for the replacement of thermoset<br />
rubbers in various applications. High performance thermoplastic<br />
elastomers, in which a highly vulcanized rubbery polymer is intimately<br />
dispersed in a thermoplastic matrix, are generally known as thermoplastic<br />
vulcanizates. Hydrosilylation crosslinking of a rubber acts via the unsaturated<br />
groups present from norbornene <strong>and</strong> diene components. Even at low<br />
concentrations of hydrosilylation agent <strong>and</strong> catalyst, a rubber can be fully<br />
crosslinked in a dynamic vulcanization process <strong>and</strong> provide a thermoplastic<br />
elastomer product with excellent physical properties <strong>and</strong> oil resistance.<br />
Suitable hydrosilylation agents are methylhydrogen polysiloxanes,<br />
methylhydrogen dimethyl-siloxane copolymers, bis(dimethylsilyl)alkanes,<br />
<strong>and</strong> bis(dimethylsilyl)benzene. 27 Platinum catalyst concentrations of 0.1<br />
to 4 ppm are sufficient. The preparation is done by mixing the rubber<br />
<strong>and</strong> silicone hydride at 180°C. Then a solution of the platinum catalyst is<br />
added. The rubber is dynamically vulcanized by mixing until maximum<br />
torque is reached.
336 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
8.6 PROPERTIES<br />
8.6.1 Silicone Rubber<br />
Silicone rubber consists essentially of silicone polymers <strong>and</strong> fillers. Silicone<br />
rubber formulations with molecular weights of more than 100 kDalton<br />
<strong>and</strong> can flow, in contrast to other polymers.<br />
8.6.1.1 HTV-silicone rubber<br />
Silicone polymers for solid silicone rubber (HTV-silicone rubber) have<br />
molecular weights of 500 kDalton to 1000 kDalton, yet exhibit a pasty<br />
consistency.<br />
8.6.1.2 RTV-silicone rubber<br />
Pourable silicone rubber (RTV-silicone rubber) has a liquid consistency<br />
<strong>and</strong> molecular weights in the range of 10 kDalton to 20 kDalton.<br />
8.6.2 Thermal Properties<br />
The service temperatures of silicones cover a wide range, from −60 to<br />
+250°C. Silicone rubber retains its elasticity to temperatures down to<br />
−60°C. The glass transition temperature is 120°C. At temperatures greater<br />
than 150 °C silicone rubbers are superior to other elastomers with respect to<br />
their thermal properties. 28 Silicone rubber exhibits a flash point of 750°C<br />
<strong>and</strong> an excellent flame retardancy. However, on combustion, it releases<br />
toxic or corrosive gases.<br />
8.6.2.1 Boron Siloxane Copolymers<br />
<strong>Polymers</strong> containing boron within the polymer are high temperature oxidatively<br />
stable materials. It has been known that the addition of a carborane<br />
within a siloxane polymer significantly increases the thermal stability of<br />
such siloxane polymers. 29 Hybrids of organic <strong>and</strong> inorganic components,<br />
made from 1,7-Bis(chlorotetramethyldisiloxy)-m-carborane, 1,3-dichlorotetramethyldisiloxane<br />
<strong>and</strong> 1,4-dilithio-1,3-butadiyne are shown in Figure<br />
8.7. Oxidative crosslinking in air is found for poly(m-carborane-di-methylsiloxane)<br />
around 420°C. 21 Such polymers can be converted into ceramics
Silicones 337<br />
H 3 C<br />
Si<br />
CH 3<br />
CH 3<br />
Si O<br />
CH 3<br />
CH 3<br />
Si C<br />
CH 3<br />
Z<br />
CH 3<br />
Si O<br />
CH 3<br />
CH 3<br />
Si Cl<br />
CH 3<br />
Cl C<br />
H 3 C<br />
O<br />
Si<br />
C<br />
CH 3<br />
C<br />
Z=B 10 H 10<br />
C<br />
C<br />
H 3 C<br />
Si<br />
CH 3<br />
Li<br />
C C C C Li<br />
O<br />
H 3 C<br />
Si<br />
CH 3<br />
CH 3 CH 3<br />
C<br />
C<br />
Z<br />
Cl<br />
Si O Si Cl<br />
H 3 C<br />
Si<br />
CH 3<br />
CH 3 CH 3<br />
O<br />
H 3 C<br />
Si<br />
CH 3<br />
B<br />
B<br />
C<br />
B<br />
C<br />
B<br />
B<br />
B<br />
B<br />
B<br />
B<br />
B<br />
Figure 8.7: <strong>Polymers</strong> from 1,7-Bis(chlorotetramethyldisiloxy)-m-carborane,<br />
1,3-dichlorotetramethyldisiloxane <strong>and</strong> 1,4-dilithio-1,3-butadiyne
338 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
by pyrolysis. Carbon fibers coated with poly(carborane-siloxane-acetylene)<br />
can be protected against oxidation at elevated temperatures. 30<br />
8.6.2.2 Microcellular Ceramics<br />
Microcellular foams were produced by means of poly(methyl methacrylate)<br />
as a sacrificial templating agent. Poly(methyl methacrylate) microbeads,<br />
were mixed in with a methylsilicone resin powder. The samples<br />
were heated up to 300°C <strong>and</strong> after one hour pyrolyzed at 1200°C. A silicon<br />
oxycarbide (SiOC) ceramic microcellular foam was obtained. 31<br />
8.6.3 Electrical Properties<br />
Silicone rubbers <strong>and</strong> resins are very efficient in insulating. The dielectric<br />
strength, the resistivity, <strong>and</strong> the dielectric constant do not change significantly<br />
with temperature.<br />
8.6.4 Surface Tension Properties<br />
Unmodified silicones exhibit hydrophobic properties. When spread out<br />
as films they impart water repellency to the carrier material. The surface<br />
tension is only around 30 mN/m.<br />
Silazanes significantly improve water-repellent properties of silicone<br />
resins. 19 Examples of hexaorganodisilazanes include hexamethyldisilazane,<br />
1,3-dihexyltetramethyldisilazane, 1,3-di-tert-butyltetramethyldisilazane,<br />
1,3-di-n-butyltetramethyldisilazane, <strong>and</strong> 1,3-diphenyltetramethyldisilazane.<br />
8.6.5 Antioxidants<br />
Iron-containing polysilazanes exhibit an antioxidation effect on silicone oil<br />
<strong>and</strong> rubber. 32 This type of polymer was synthesized by the polycondensation<br />
of silazane lithium salts with iron trichloride. The synthesis is shown<br />
in Figure 8.8. The gelling time of a silicone oil increased from 3 to 1000<br />
hours at 300°C in air by an addition of 5% of polysilazane.<br />
8.6.6 Gas Permeability<br />
Silicones have an extraordinarily high gas permeability. They find use in<br />
medical applications, e.g., as contact lenses, so that the oxygen in air can
Silicones 339<br />
H<br />
Li<br />
H 3 C CH 3 H<br />
N<br />
3 C CH 3<br />
N<br />
Si Si BuLi Si Si<br />
H 3 C CH 3<br />
H 3 C CH 3<br />
N N<br />
N N<br />
H Si H<br />
H Si H<br />
H 3 C CH 3<br />
H 3 C CH 3<br />
Li<br />
H 3 C CH 3<br />
N<br />
Si Si<br />
H 3 C CH 3<br />
N N<br />
H Si Li<br />
H 3 C CH 3<br />
BuLi<br />
BuLi<br />
Li<br />
H 3 C CH 3<br />
N<br />
Si Si<br />
H 3 C CH 3<br />
N N<br />
Li Si Li<br />
H 3 C CH 3<br />
H 3<br />
C CH<br />
Si Si 3<br />
N<br />
H 3 C CH 3<br />
Li<br />
H 3 C<br />
CH 3<br />
Si<br />
N<br />
Li<br />
Si<br />
CH 3<br />
CH 3<br />
FeCl 3<br />
H 3 C<br />
Li Si<br />
N<br />
H 3 C<br />
Si<br />
H 3 C<br />
CH 3<br />
H 3 C CH<br />
Si Si 3<br />
N<br />
H 3 C CH 3<br />
Li<br />
H 3 C<br />
CH 3 Fe H 3 C<br />
Si<br />
N<br />
Si<br />
Li<br />
CH 3<br />
Li<br />
H 3 C<br />
N Si<br />
Si<br />
CH 3 H 3 C<br />
CH 3<br />
Figure 8.8: Synthesis of Iron-containing Polysilazanes
340 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
contact the cornea of the eye. Another medical application is the use as<br />
permeable membrane in heart-lung machines.<br />
8.6.7 Weathering<br />
Silicone rubber is highly resistant to ozone <strong>and</strong> radiation. Therefore, it<br />
exhibits good weathering properties.<br />
8.7 APPLICATIONS AND USES<br />
Silicone products are used for a wide variety of applications, including<br />
building <strong>and</strong> construction material, medical applications, sealing, impregnation,<br />
putty, surface treatments, <strong>and</strong> painting applications. Silicone rubbers<br />
can be fabricated into tubing, hose, gaskets, <strong>and</strong> seals.<br />
Silicone oils are oligomeric chains of poly(dimethylsiloxane). The<br />
fluids are thermally stable <strong>and</strong> chemically resistant. They can serve as<br />
excellent lubricants.<br />
8.7.1 Antifoaming Agents<br />
The low surface tension enables silicones to be used as antifoaming agents,<br />
foam stabilizers, <strong>and</strong> free-flowing agents, e.g., in paints.<br />
8.7.1.1 Antifoaming Agents<br />
Suspension polymerization of PVC, silicone antifoaming agents are an important<br />
constituent. Also, foaming in spinning baths of man-made fibers<br />
can be controlled by silicone antifoaming agents.<br />
8.7.2 Release Agents<br />
8.7.2.1 Mold Release Agents<br />
Silicones are used as mold release agents in the rubber <strong>and</strong> plastics industries.<br />
Molds made from silicone rubber itself are common.<br />
Silicone resins are typically applied to surfaces by dissolving the<br />
silicone resin in volatile solvents. Evaporation of the solvent leaves behind<br />
the silicone resin in the desired location, e.g., on the surface of the mold<br />
for release, or in the cavities <strong>and</strong> interstices of the port as a sealant. Then,
Silicones 341<br />
with the application of heat or chemicals, the resin is cured in-situ, forming<br />
a hard, polymeric network.<br />
Waterborne silicone release agents are common. An advantage of<br />
using water as a carrier is that the presence of water can prevent or delay<br />
silanol condensation of the resin. A catalyst may be added <strong>and</strong> stored in a<br />
water-based composition without inducing immediate curing. Hence, the<br />
use of water as a carrier improves the shelf life of the composition.<br />
The most significant difficulty associated with using water as a carrier<br />
is that silicone resins are relatively immiscible in water. Water-based<br />
silicone resin compositions can be formulated using conventional surfactants.<br />
Large amounts of surfactant, however, are usually required, <strong>and</strong> the<br />
dispersion formed may not be very stable. The dispersion can be stabilized<br />
with a hydrophobically modified polycarboxylic acid. 33<br />
8.7.2.2 Paper Release Agents<br />
Crosslinkable silicone polymers are used as silicone release papers. These<br />
have a wide range of applications for labels <strong>and</strong> coatings.<br />
8.7.3 Sealing <strong>and</strong> Jointing Materials<br />
Silicone seals have found widespread uses in cars, gaskets, household engines,<br />
<strong>and</strong> medical devices. Silicone jointing materials are used for expansion<br />
joints on building facades, connecting aluminum or plastic, <strong>and</strong> in the<br />
sanitary field, e.g., for bathroom tiles. Various silicone rubber grades have<br />
been developed with different curing systems.<br />
8.7.4 Electrical Industry<br />
The high insulating power of silicones is appreciated in the electrical industry.<br />
<strong>Applications</strong> are in cables, electrical motors, seals, <strong>and</strong> heating<br />
elements. Silicone rubber rollers are used in photocopying devices, <strong>and</strong><br />
facsimile devices.<br />
8.7.5 Medical <strong>Applications</strong><br />
Silicones are mostly inert to living organisms. They are considered nontoxic<br />
materials <strong>and</strong> can be used in pharmaceutical <strong>and</strong> medical applications.
342 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
8.8 SPECIAL FORMULATIONS<br />
8.8.1 Polyimide Resins<br />
Polyimide resins are commonly used as materials for printed circuit<br />
boards <strong>and</strong> heat-resistant adhesive tapes because of their high<br />
heat resistance <strong>and</strong> superior electrical insulation properties. Common<br />
basic materials are 3,3 ′ ,4,4 ′ -diphenylsulfone tetracarboxylic dianhydride<br />
(DSDA) 4,4 ′ -hexafluoropropylidenebisphthalic dianhydride (6FDA),<br />
2,2-bis[4-(4-aminophenoxy)phenyl]propane (BAPP) <strong>and</strong> 3,3 ′ -dihydroxy-<br />
4,4 ′ -diaminobiphenyl (HAB).<br />
They are used as resin varnish to form surface protective films <strong>and</strong><br />
interlayer insulating films of electronic parts <strong>and</strong> semiconductor materials.<br />
Commonly a solution is prepared by dissolving a polyimide precursor such<br />
as polyamic acid.<br />
The solution is coated on a substrate, followed by removal of the<br />
solvent. Then high-temperature treatment effects the dehydration cyclization<br />
<strong>and</strong> the product obtained is used as polyimide resin. To improve the<br />
solubility of a polyimide resin in solvents, improve its adhesive force to<br />
substrates <strong>and</strong> impart flexibility, a siloxane group can be introduced into<br />
the polyimide skeleton.<br />
Such siloxane materials are diaminosiloxanes, i.e., straight chain silicones<br />
having amino groups at both terminals. Therefore, types with a<br />
small content of cyclic siloxane oligomers have been developed. 34<br />
8.8.2 Thermal Transfer Ribbons<br />
Thermal transfer printing is advantageous because relatively low noise levels<br />
are attained during printing. Thermal transfer printing is widely used<br />
in special applications such as printing of machine readable bar codes <strong>and</strong><br />
magnetic alpha-numeric characters. Most thermal transfer ribbons employ<br />
poly(ethylene terephthalate) (PET) polyester as a substrate. The functional<br />
layer which transfers ink, also referred to as the thermal transfer layer, is<br />
deposited on one side of the substrate, <strong>and</strong> a protective backcoat is deposited<br />
on the other side of the poly(ethylene terephthalate) substrate.<br />
Untreated poly(ethylene terephthalate) will not pass under a thermal<br />
print head without problems. The side of the poly(ethylene terephthalate)<br />
substrate which comes in contact with the print head, i.e., the side opposite<br />
the thermal transfer layer, must be protected during the printing process.
Silicones 343<br />
Failure to do so will result in the sticking of poly(ethylene terephthalate)<br />
to the heating elements during the heating cycle. Poly(ethylene terephthalate)<br />
is also an abrasive material which will cause unacceptable wear on the<br />
print head. Therefore, conventional thermal transfer ribbons which employ<br />
a poly(ethylene terephthalate) substrate have treated backsides. The substrate<br />
is coated on the reverse side to form a barrier between the poly(ethylene<br />
terephthalate) <strong>and</strong> the print head.<br />
The backcoats are usually comprised of silicone polymers. The most<br />
common backcoats are silicone oils <strong>and</strong> UV cured silicones. The silicone<br />
oils can be delivered directly to the PET substrate or via an organic solvent.<br />
However, for environmental reasons solvent-free coatings are used.<br />
A water-soluble silicone block copolymer consists of silicone resin blocks<br />
<strong>and</strong> water-soluble poly(ethylene oxide) blocks or poly(propylene oxide)<br />
blocks. 35<br />
8.8.3 Self-Assembly Systems<br />
The adhesion between a substrate <strong>and</strong> a polymer can be improved by using<br />
molecular self-assembling polymers. Typical self-assembly systems<br />
include silanes on hydroxylated substrates, such as glass surfaces or silicon<br />
wafers. The mechanical stability of a self-assembled polymer film can<br />
be increased by incorporating sticker groups in the polymer chain to introduce<br />
additional interactions between the sticker groups <strong>and</strong> the substrate<br />
solid surface.<br />
This is why silane functionalized poly(styrene) <strong>and</strong> poly(methyl<br />
methacrylate) were polymerized in the presence of a silane coupling agent,<br />
mercaptopropyltrimethoxysilane (MPS), which is also an effective chain<br />
transfer agent in the radical polymerization. 36<br />
8.8.4 Plasma Grafting<br />
Cornstarch granules could be surface functionalized in a high frequency<br />
plasma with ethylene diamine. In the second step the material was grafted<br />
with dichlorodimethylsilane.<br />
A poly(dimethylsiloxane) graft-copolymer layer on the modified surface<br />
was detected. 37 The starch graft-copolymer might find use as a reinforcing<br />
component in silicone-rubber materials.
344 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
8.8.5 Antifouling Compositions<br />
Aquatic animal <strong>and</strong> plant organisms such as barnacles, oysters, ascidians,<br />
polyzoans, serupulas, sea lettuces <strong>and</strong> green layers adhere <strong>and</strong> grow on the<br />
surface of marine structures, resulting in damage. For example, the aquatic<br />
organisms can adhere to the bottom of a ship, increasing the frictional resistance<br />
between the ship body <strong>and</strong> water. The increased resistance results<br />
in higher fuel costs. Some industrial plants use sea water for cooling.<br />
Fouling of intake pipes by aquatic animals <strong>and</strong> plants can hinder<br />
the induction of cooling water resulting in a drop in cooling effectiveness.<br />
A wide range of marine structures such as undersea construction, piers,<br />
buoys, harbor facilities, fishing nets, ships, marine tanks, water conduit<br />
raceway tubes of power plants <strong>and</strong> coastal industrial plants are affected.<br />
8.8.5.1 Biopolymers<br />
Marine organisms are initially attracted to <strong>and</strong> subsequently attach to a surface<br />
by chemical <strong>and</strong> physical means. Biopolymers such as polypeptides<br />
<strong>and</strong> polysaccharides comprise the outermost layer of marine organisms,<br />
<strong>and</strong> in some cases the marine organism exudes a glue, which is typically<br />
comprised of similar material, by which it attaches to a substrate.<br />
Biopolymers are very polar, <strong>and</strong> initial physical attachment to a substrate<br />
easily occurs when the substrate contains polar groups to which these<br />
biopolymers can form hydrogen-bonds. Further chemical attachment can<br />
take place by reactions between the biopolymers <strong>and</strong> a substrate. A hydrophobic<br />
surface is one which contains very little to no polar groups; thus,<br />
a hydrophobic surface expresses very few toeholds for marine organisms to<br />
adhere. The only type of attraction would be Van der Waals forces, which<br />
are very weak.<br />
8.8.5.2 Toxicants<br />
Various antifouling compositions have been developed to prevent the adherence<br />
of the aquatic organisms. Toxicants containing copper, tin, arsenic<br />
<strong>and</strong> mercury, <strong>and</strong> others been proposed. Further, strychnine, atropine, creosote,<br />
<strong>and</strong> phenol have been proposed.<br />
However, even the effective compositions have disadvantages. These<br />
compositions prevent fouling by a toxic mechanism. Effectiveness of the
Silicones 345<br />
compositions requires that a lethal concentration of poison be maintained<br />
in the water immediately adjacent to the surface of the marine structure.<br />
Eventually, the poison is completely leached into the water <strong>and</strong> the<br />
composition is exhausted <strong>and</strong> must be replaced. Further, the poisons are<br />
toxic to humans <strong>and</strong> aquatic life <strong>and</strong> can be a major source of pollution in<br />
busy harbors <strong>and</strong> in waterways.<br />
8.8.5.3 Fouling Release Coatings<br />
Fouling release coatings, i.e., coatings which do not allow organisms to<br />
adhere to the marine body surface, have been proposed as alternatives to<br />
the toxicity-based antifouling agents.<br />
Particularly suitable are curable fluorinated silicone resins formed<br />
by replacing some but not all of SiH groups in an end-capped fluoroalkyl<br />
group-containing polyalkylhydrosiloxane. Otherwise, a fluorinated silicon<br />
resin can be blended with a non-fluorinated organopolysiloxane resin prior<br />
to crosslinking.<br />
Examples of suitable unsaturated fluoroalkyls include nonafluorohexene,<br />
1H-1H-2H-perfluoroheptene, 1H-1H-2H-perfluorooctene, 1H-1H-<br />
2H-perfluorononene <strong>and</strong> 3,3,4,4,5,5,5-heptafluoro-1-pentene.<br />
Fluorosilicons are prepared by reacting a polyalkylhydrosiloxane<br />
<strong>and</strong> an unsaturated fluoroalkyl compound. A suitable catalyst is an organic<br />
transition metal salt, such as zinc octoate.<br />
The fluorinated silicon resin is then crosslinked either by the pendant<br />
groups of the silicon resin itself, or with added compounds.<br />
Such added components can be methyltriethoxysilane or octyl triethoxysilane<br />
or a tetraethoxysilane or a fluoroalkyltriethoxysilane.<br />
The coating consists of more than one layer, an anticorrosive layer,<br />
the adhesion promoting layer, <strong>and</strong> the release layer. Adhesion promoting<br />
layers include a moisture curable grafted copolymer that further includes<br />
poly(dialkylsiloxane) <strong>and</strong> n-butyl acrylate, styrene, vinyl chloride <strong>and</strong> vinylidene<br />
chloride that is grafted onto the siloxane backbone. An aminofunctionalized<br />
polysiloxane is active as adhesion promoter. The release<br />
layer consists of the fluorinated polysiloxane. 38<br />
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elastomer. US Patent 6 251 998, assigned to Advanced Elastomer<br />
Systems, L.P. ; Exxon Chemical Patents, Inc., June 26 2001.
348 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
28. P. R. Dvornic <strong>and</strong> R. W. Lenz. High Temperature Siloxane Elastomers.<br />
Hüthig & Wepf, Basel, New York, 1990.<br />
29. T. M. Keller <strong>and</strong> D. Y. Son. High temperature ceramics derived from linear<br />
carborane-(siloxane or silane)-acetylene copolymers. US Patent 6 265 336,<br />
assigned to The United States of America as represented by the Secretary of<br />
the Navy (Washington, DC), July 24 2001.<br />
30. T. M. Keller. Oxidative protection of carbon fibers with poly(carborane-siloxane-acetylene).<br />
Carbon, 40(3):225–229, March 2002.<br />
31. P. Colombo, E. Bernardo, <strong>and</strong> L. Biasetto. Novel microcellular ceramics<br />
from a silicone resin. J. Am. Ceram. Soc., 87(1):152–154, January 2004.<br />
32. Y. M. Li, Z. M. Zheng, C. H. Xu, C. Y. Ren, Z. J. Zhang, <strong>and</strong> Z. M. Xie. Synthesis<br />
of iron-containing polysilazane <strong>and</strong> its antioxidation effect on silicone<br />
oil <strong>and</strong> rubber. J. Appl. Polym. Sci., 90(1):306–309, October 2003.<br />
33. J. Wang. Water-based silicone resin compositions. US Patent 5 804 624,<br />
September 8 1998.<br />
34. M. Sugo <strong>and</strong> H. Kato. Polyimide silicone resin, process for its production,<br />
<strong>and</strong> polyimide silicone resin composition. US Patent 6 538 093, assigned to<br />
Shin-Etsu Chemical Co., Ltd. (Tokyo, JP), March 25 2003.<br />
35. J. D. Roth. Water soluble silicone resin backcoat for thermal transfer ribbons.<br />
US Patent 6 245 416, assigned to NCR Corporation (Dayton, OH), June 12<br />
2001.<br />
36. F. Zhou, W. M. Liu, T. Xu, S. J. Liu, M. Chen, <strong>and</strong> J. X. Liu. Preparation<br />
of silane-terminated polystyrene <strong>and</strong> polymethylmethacrylate self-assembled<br />
films on silicon wafer. J. Appl. Polym. Sci., 92(3):1695–1701, May 2004.<br />
37. Y. H. C. Ma, S. Manolache, M. Sarmadi, <strong>and</strong> F. S. Denes. Synthesis of<br />
starch copolymers by silicon tetrachloride plasma-induced graft polymerization.<br />
Starch-Stärke, 56(2):47–57, February 2004.<br />
38. A. E. Mera <strong>and</strong> K. J. Wynne. Fluorinated silicone resin fouling release composition.<br />
US Patent 6 265 515, assigned to The United States of America as<br />
represented by the Secretary of the Navy (Washington, DC), July 24 2001.
9<br />
Acrylic Resins<br />
Acrylic resins are polymers of acrylic or methacrylic esters. They are<br />
sometimes modified with monomers such as acrylonitrile <strong>and</strong> styrene. The<br />
most common acrylates are methyl acrylate, ethyl acrylate, n-butyl acrylate<br />
<strong>and</strong> 2-ethylhexyl acrylate. Methacrylates include methyl methacrylate,<br />
ethyl methacrylate, butyl methacrylate, <strong>and</strong> higher alcohol esters.<br />
The resins are used either as molding powders or casting syrups.<br />
Acrylic resins are often used as hybrid resins in combination with urethanes,<br />
epoxides <strong>and</strong> silicones.<br />
Since coatings are not the primary goal of this topic, coating applications<br />
will be dealt with only marginally, even when acrylic resins contribute<br />
highly to this topic. Acrylic resins are also widely used for dental applications.<br />
We treat this topic because of its importance in a special chapter.<br />
Here we focus on non-dental applications of acrylic resins.<br />
An overview on acrylic <strong>and</strong> methacrylic ester polymers is given in<br />
the literature. 1, 2<br />
9.1 HISTORY<br />
Acrylic acid was obtained through the air oxidation of acrolein by Redtenbacher<br />
in 1843. Methacrylic acid was first prepared in 1865. Otto Röhm<br />
observed the polymerization of acrylics. The production of acrylates<br />
started in 1927 by Röhm&Haas. In 1936 poly(methyl methacrylate) was<br />
prepared by a casting process.<br />
349
350 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
CH 2 CH C<br />
O CH 3<br />
O<br />
CH 2 CH C<br />
O CH 2 CH 3<br />
Methyl acrylate<br />
Ethyl acrylate<br />
O<br />
CH 2 CH C<br />
O CH 2 CH CH 2 CH 2 CH 2 CH 2 CH 3<br />
CH 2<br />
CH 3<br />
CH 2<br />
2 CH 3<br />
2-Ethylhexyl acrylate<br />
O<br />
CH C O<br />
O<br />
CH 2<br />
CH 2 CH C O CH 2 C CH<br />
CH 2 CH C O<br />
O CH 2<br />
Trimethylolpropane triacrylate<br />
Figure 9.1: Acrylate-based Monomers<br />
9.2 MONOMERS<br />
A large variety of monomers is known, because of the possibility of esterifying<br />
the acrylic acid <strong>and</strong> methacrylic acid with various alcohols. The<br />
most common monomers are shown in Table 9.1. Some acrylate-based<br />
monomers are shown in Figure 9.1.<br />
9.2.1 Specialities<br />
9.2.1.1 Cyclohexyl methacrylates<br />
<strong>Polymers</strong> containing cyclohexyl methacrylate <strong>and</strong> related compounds such<br />
as 4-methylcyclohexylmethyl methacrylate exhibit high weather resistance.<br />
This is due to its low hygroscopic functional group. It is used for<br />
coating materials.
Acrylic Resins 351<br />
Table 9.1: Monomers for Acrylic Resins<br />
Monomer Remarks Reference<br />
Acrylic Monomers<br />
Acrylic acid<br />
Methyl acrylate<br />
Ethyl acrylate<br />
n-Butyl acrylate<br />
2-Ethylhexyl acrylate<br />
Trimethylolpropane triacrylate (TMPTA)<br />
a 3<br />
Aziridine derivatives<br />
a 4<br />
Methacrylic Monomers<br />
Methyl methacrylate<br />
b<br />
Ethyl methacrylate<br />
2-Hydroxyethyl methacrylate (HEMA)<br />
n-Butyl methacrylate<br />
c<br />
Ethylene glycol dimethacrylate<br />
a<br />
Poly(ethylene glycol)dimethacrylate<br />
3-Methacryloxypropyl-trimethoxysilane (MPTS)<br />
5<br />
Cyclohexyl methacrylate<br />
d 6<br />
4-Methylcyclohexylmethyl methacrylate<br />
7<br />
Methacryloyl isocyanate<br />
7<br />
2-Methacryloyloxyethyl isocyanate<br />
7<br />
Methyl N-methacryloylcarbamate<br />
8<br />
Phenyl N-methacryloylcarbamate<br />
8<br />
2-Ethylhexyl N-methacryloylcarbamate<br />
9<br />
2-Isocyanatoethyl methacrylate (IEM)<br />
10<br />
a Crosslinker<br />
b St<strong>and</strong>ard<br />
c Flexible<br />
d Improved weatherability
352 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
9.2.1.2 Methacryloyl Isocyanate <strong>and</strong> Derivatives<br />
Alkenoylcarbamates can be readily polymerized by themselves or with any<br />
other vinyl compounds. The carbamates formed from alcohols with a small<br />
number of carbon atoms are available in a stable solid form under the atmospheric<br />
condition <strong>and</strong> can be dissolved easily in various solvents.<br />
The acylurethane structure contributes to an enhancement of cohesion.<br />
Therefore, copolymers containing alkenoylcarbamate units show various<br />
advantageous properties such as high elasticity <strong>and</strong> good adhesion.<br />
The introduction of an epoxy or aziridino group introduces further<br />
reactive moieties. The modification to a blocked isocyanate structure provides<br />
the alkenoylcarbamate compounds with the latent reactivity of an<br />
isocyanate group, which will be actualized from the blocked isocyanate<br />
structure under heating.<br />
Methyl N-methacryloylcarbamate, phenyl N-methacryloylcarbamate,<br />
benzyl N-methacryloylcarbamate, <strong>and</strong> a series of other methacryloyl<br />
carbamates can be synthesized from methacryloyl isocyanate by adding the<br />
appropriate alcohols to methacryloyl isocyanate. 8 The synthesis is shown<br />
in Figure 9.2. The reaction is conducted at low temperatures. Also an exchange<br />
of the alcohol group in the carbamate is possible. For example,<br />
ethyl N-methacryloylcarbamate can be reacted with 2-ethylhexyl alcohol<br />
in the presence of a radical polymerization inhibitor such as hydroquinone<br />
at 120°C. The ethoxy moiety is then replaced by the 2-ethylhexyloxy moiety<br />
to result in 2-ethylhexyl N-methacryloylcarbamate. This product is a<br />
viscous liquid. 9<br />
9.2.2 Synthesis<br />
9.2.2.1 Monomers<br />
Acrylic acid is synthesized by the oxidation of propene via acrolein.<br />
Methyl methacrylate is synthesized from acetone via the acetone cyanhydrin<br />
(ACH). The reactions are shown in Figure 9.3. The conventional<br />
process for the synthesis of methyl methacrylate runs via the acetone cyanhydrin.<br />
Other technical processes include<br />
• The ACH-based process (Röhm&Haas, Mitsubishi Gas Chemical),<br />
• The i-butylene oxidation process (Lucky, Japan Methacrylic),<br />
• The tert-butanol oxidation process (Kyodo, Mitsubishi Rayon),
Acrylic Resins 353<br />
CH 2<br />
CH 3<br />
C C N C O<br />
CH 3 OH<br />
CH 2<br />
CH 3 H<br />
C C N C O<br />
O<br />
O<br />
O<br />
CH 3<br />
N-Methacryloylcarbamate<br />
CH 2<br />
CH 3<br />
C C N C O<br />
OH<br />
CH 2<br />
CH 3 H<br />
C C N C O<br />
O<br />
O<br />
O<br />
Phenyl N-methacryloylcarbamate<br />
Figure 9.2: Synthesis of Methyl N-methacryloylcarbamate <strong>and</strong> Phenyl N-methacryloylcarbamate<br />
8<br />
• The propyne carbonylation (Shell, ICI), <strong>and</strong><br />
• The hydrocarbonylation of ethene. 11<br />
9.2.2.2 Esterification<br />
The reaction of methacrylic acid with an alcohol results in the respective<br />
ester. Also, an olefin can be added to the acid in the presence of anhydrous<br />
catalysts. Ethylene oxide reacts to form the hydroxy alkyl esters. Diazomethane<br />
reacts to the methyl esters. The reactions are shown in Figure 9.4.<br />
9.2.3 Manufacture<br />
Various structural elements, such as rods, sheets, tubes, <strong>and</strong> molding powders<br />
are produced by bulk polymerization. The most common method for<br />
the production of sheets is the batch cell method. The polymerization process<br />
releases a lot of heat <strong>and</strong> has to be carried out slowly, in order to<br />
avoid an adverse effect on the optical properties. If the polymerization in<br />
bulk quantities proceeds too fast, even the boiling point can be crossed <strong>and</strong>
354 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O 2<br />
CH 2 CH C<br />
O<br />
CH 2 CH CH 3 CH 2 CH C<br />
H<br />
O<br />
CH 2 CH C<br />
H<br />
O 2<br />
O<br />
OH<br />
CH 3<br />
CH 3<br />
C O HCN HO C C N H CH<br />
2SO 2 4<br />
C C NH 2<br />
CH 3 CH 3<br />
CH 3<br />
H 2 SO 2<br />
CH 3<br />
OH<br />
CH 2<br />
CH 3<br />
C C<br />
O<br />
OCH 3<br />
Figure 9.3: Synthesis of Acrylic acid <strong>and</strong> Methyl methacrylate
Acrylic Resins 355<br />
CH 2<br />
CH 3<br />
C C<br />
O<br />
CH 3<br />
OH + HO R CH 2 C C<br />
O<br />
OR<br />
CH 2<br />
CH 3<br />
C C<br />
OH + CH 2 CH R<br />
O<br />
CH 2<br />
CH 3<br />
C C<br />
O<br />
CH 2 CH 2 R<br />
O<br />
CH 2<br />
CH 3<br />
C C<br />
O<br />
O<br />
OH + H 2 C CH 2<br />
CH 2<br />
CH 3<br />
C C<br />
O<br />
O CH 2 CH 2 OH<br />
CH 2<br />
CH 3<br />
C C<br />
CH 3<br />
OH + CH 2 N 2 CH 2 C C<br />
OCH 3<br />
O<br />
O<br />
Figure 9.4: Esterification Reactions of Methacrylic Acid
356 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 9.2: Ultraviolet Absorbers for Acrylic Resins 12<br />
Compound<br />
Benzotriazole Ultraviolet Absorbers<br />
2-(5-Methyl-2-hydroxyphenyl)benzotriazole<br />
2-[2-Hydroxy-3,5-bis(α,α-dimethylbenzyl)phenyl]-2H-benzotriazole<br />
2-(3,5-Di-tert-butyl-2-hydroxyphenyl)benzotriazole<br />
2-(3-tert-Butyl-5-methyl-2-hydroxyphenyl)-5-chlorobenzothiazole<br />
2-(3,5-Di-tert-Butyl-2-hydroxyphenyl)-5-chlorobenzothiazole<br />
2-(3,5-Di-tert-amyl-2-hydroxyphenyl)benzotriazole<br />
2-(2 ′ -Hydroxy-5 ′ -tert-octylphenyl)benzotriazole<br />
2-Hydroxybenzophenone Ultraviolet Absorbers<br />
2-Hydroxy-4-methoxybenzophenone<br />
2-Hydroxy-4-octoxybenzophenone<br />
2,4-Dihydroxybenzophenone<br />
2-Hydroxy-4-methoxy-4 ′ -chlorobenzophenone<br />
2,2 ′ -Dihydroxy-4-methoxybenzophenone<br />
2,2 ′ -Dihydroxy-4,4 ′ -dimethoxybenzophenone<br />
Salicylic Acid Phenyl Ester Ultraviolet Absorbers<br />
p-tert-Butylphenyl salicylate<br />
p-Octylphenyl salicylate<br />
thus bubbles are formed. Inhomogeneous temperature distribution during<br />
polymerization my cause streaks in the material.<br />
9.3 SPECIAL ADDITIVES<br />
9.3.1 Ultraviolet Absorbers<br />
Examples of ultraviolet absorbers are shown in Table 9.2.<br />
9.3.2 Flame Retardants<br />
Flame resistance can be imparted by incorporating certain organic phosphoric<br />
acid esters to acrylic resins. Some flame retardants are shown in<br />
Table 9.3 <strong>and</strong> in Figure 9.5.<br />
However, these organic phosphoric acid esters usually have a plasticizing<br />
effect. They are likely not only to substantially lower the heat<br />
distortion temperature of the acrylic resin products, but also to lower its
Acrylic Resins 357<br />
Table 9.3: Flame Retardants13, 14<br />
Compound Remarks Reference<br />
Phosphoric acid esters<br />
13<br />
Chlorinated polyphosphates<br />
13<br />
Halogenated polyphosphonate<br />
13<br />
Alkyl acid phosphate Synergist<br />
13<br />
Tetrabromobisphenol A<br />
14<br />
2,2-Bis(4-hydroxy-3,5-dibromophenyl)propane<br />
14<br />
Tricresyl phosphate<br />
14<br />
Tris(2-chloroethyl)phosphate<br />
14<br />
Antimony trioxide Inorganic<br />
14<br />
Zirconium hydroxide Inorganic<br />
14<br />
Barium metaborate Inorganic<br />
14<br />
Tin oxide Inorganic<br />
14<br />
O O O<br />
CH 2 O P O CH P O CH P O CH 2<br />
CH 2 CH 2 CH 3 O CH 3 O CH 2<br />
Cl CH 2<br />
Cl<br />
CH 2<br />
CH 2<br />
CH 2<br />
CH 2<br />
Cl<br />
Cl Cl<br />
Figure 9.5: Chlorinated Polyphosponate (Phosgard C-22 R, Monsanto)
358 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 9.4: Global Production Data of Important Monomers <strong>and</strong> <strong>Polymers</strong><br />
15 Monomer Mill. Metric tons Year Reference<br />
Methyl methacrylate 2 2002<br />
16<br />
Acrylic surface coatings 0.92 2003<br />
17<br />
Acrylic resins <strong>and</strong> plastics 0.85 2000<br />
18<br />
mechanical strength. Further, the water absorptivity of the resin products<br />
tends to increase by the incorporation of such flame retardants, <strong>and</strong> when<br />
used outdoors, the resin products are likely to undergo deformation or crazing<br />
upon absorption of water.<br />
For a copolymer of methyl methacrylate, α-methylstyrene, styrene,<br />
maleic anhydride, <strong>and</strong> methacrylic acid, a synergism has been observed.<br />
When two types of flame retardants, i.e., a halogen-containing condensed<br />
phosphoric acid ester or a halogenated polyphosphonate <strong>and</strong> an alkyl acid<br />
phosphonate, are combined, superior flame resistance <strong>and</strong> physical properties<br />
will be imparted by the synergistic effect of the components.<br />
Here, it is possible to reduce the amount of the main flame retardant<br />
to a level of about 20% even when the flame resistance should meet the<br />
st<strong>and</strong>ard of V-0 of the UL St<strong>and</strong>ards. 19<br />
Therefore, it is possible to avoid the deterioration of the physical<br />
properties, particularly the deterioration of the heat resistance, which is a<br />
serious problem when a great amount of the flame retardant is added. 13<br />
9.3.3 Production Data of Important Monomers<br />
Global production data of the most important monomers used for acrylic<br />
ester resins are shown in Table 9.4.<br />
9.4 CURING<br />
The polymerization of acrylic resins occurs essentially by a radical mechanism.<br />
9.4.1 Initiator Systems<br />
Traditional radical polymerization initiators may be used for the casting<br />
polymerization. Common catalysts are shown in Table 9.5. Polymerization
Acrylic Resins 359<br />
Table 9.5: Polymerization Initiators for Casting<br />
Initiator<br />
Azobis-type Catalysts 13<br />
Remarks<br />
2,2 ′ -Azobis(isobutyronitrile) preferred<br />
2,2 ′ -Azobis(2,4-dimethylvaleronitrile) preferred<br />
Diacylperoxide-type Catalysts 13<br />
Lauroyl peroxide<br />
Dibenzoyl peroxide<br />
Bis(3,5,5-trimethylhexanoyl)peroxide<br />
Perester-type Catalysts 20<br />
tert-Amylperoxy-2-ethylhexanoate<br />
tert-Butylperoxy-2-ethylhexanoate<br />
Percarbonate-type Catalysts 13<br />
bis(4-tert-Butylcyclohexyl)peroxydicarbonate<br />
UV Curing Catalysts 3<br />
2,2-Dimethoxy-2-phenylacetophenone (DMPA)<br />
benzophenone (BP) <strong>and</strong><br />
methyldiethanolamine (MDEA)<br />
Acyl-phosphine oxide<br />
21<br />
preferred<br />
preferred
360 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
initiators particularly suitable for the continuous sheet-forming process are<br />
those having a decomposition temperature, at a half-life of 10 hours, in the<br />
range of 40°C to 80°C.<br />
9.4.2 Promoters<br />
Special initiator systems for cold curing were developed. An effective initiator<br />
promoter system consists of a zinc 2-ethylhexanoate solution, a cobalt<br />
2-ethylhexanoate, <strong>and</strong> as peroxide source tert-butylperoxybenzoate. 22<br />
9.5 PROPERTIES<br />
Acrylic resins are appreciated for their exceptional clarity <strong>and</strong> optical properties.<br />
Acrylics show a slow burning behavior <strong>and</strong> can be formulated as<br />
self-extinguishing.<br />
Acrylic resins are excellent in transparency, translucency, surface<br />
gloss, <strong>and</strong> weather resistance <strong>and</strong> further have a high surface hardness <strong>and</strong><br />
a superior design adaptability.<br />
Therefore, they find a wide variety of applications in interior materials<br />
for vehicles, exterior materials for household electrical appliances <strong>and</strong><br />
building materials (exterior) for example, regardless of whether they are<br />
outdoor or indoor applications.<br />
However, acrylic resins generally exhibit poor flexibility <strong>and</strong> low<br />
impact resistance <strong>and</strong>, therefore, pose a problem in that they are prone to<br />
fracture when given an extraneous load or impact.<br />
9.5.1 Electrical Properties<br />
Acrylic resins are easily electrically charged by friction because of their<br />
high surface resistivity. Thus they are deteriorated in appearance by adhesion<br />
of rubbish or dust, or they bring about an undesirable situation<br />
by electrostatic electrification in parts of electronic equipment. Antistatic<br />
properties to the acrylic resin can be imparted by 23<br />
• Kneading a surfactant with the acrylic resin, or applying a surfactant<br />
on the surface of the acrylic resin,<br />
• Kneading a vinyl copolymer having a poly(oxyethylene) chain <strong>and</strong><br />
a sulfonate, carboxylate or quaternary ammonium salt structure,<br />
with an acrylate resin,
Acrylic Resins 361<br />
• Kneading a polyether ester amide with a methyl methacrylatebutadiene-styrene<br />
copolymer,<br />
• Adding a functional polyamide elastomer,<br />
• Adding a polyamide-imide elastomer having a low content of hard<br />
segments.<br />
9.5.2 Hydrolytic <strong>and</strong> Photochemical Stability<br />
Methacrylate-based polymers have a better hydrolytic stability than the<br />
corresponding acrylate polymers. They are much more stable than vinyl<br />
acetate polymers.<br />
Acrylic <strong>and</strong> methacrylic resins are not very sensitive to ultraviolet<br />
radiation. However, ultraviolet absorbers improve stability. Adding ultraviolet<br />
absorbers, e.g., to arcylic windows, also protects the interior from<br />
UV radiation.<br />
9.5.3 Recycling<br />
Poly(methyl methacrylate) depolymerizes nearly qualitatively (ca. 96%)<br />
on pyrolysis into the monomer. This property is attractive for thermal recycling<br />
of unmixed poly(methyl methacrylate) wastes. The situation in the<br />
case of acrylates is different.<br />
9.6 APPLICATIONS AND USES<br />
Acrylic resins have been widely used as materials for various parts of electronics<br />
products, household appliances, office automation appliances, etc.<br />
because of their excellent transparency <strong>and</strong> stiffness. 23 They are used in<br />
the sanitary sector, as surrogate for ordinary glass.<br />
9.6.1 Acrylic Premixes<br />
An acrylic resin composition can be used as raw material for an acrylic<br />
premix for producing an acrylic artificial marble. Acrylic artificial marbles<br />
are obtained by blending an acrylic resin with inorganic fillers such as aluminium<br />
hydroxide. They have an excellent appearance, soft feeling <strong>and</strong><br />
weatherability <strong>and</strong> are widely used for kitchen counters, lavatory dressing<br />
tables, waterproof pans, etc.
362 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Artificial marbles are generally produced by filling a slurry mold.<br />
This mold is obtained by dispersing inorganic fillers in an acrylic syrup.<br />
The filled slurry must be cured at relatively low temperature. The acrylic<br />
syrup has a comparatively low boiling temperature. Consequently a long<br />
time is required for molding which causes low productivity. To overcome<br />
these drawbacks, the acrylic syrup can be blended with a crosslinked resin<br />
powder having a specific degree of swelling.<br />
On the other h<strong>and</strong>, an acrylic premix for an artificial marble, with excellent<br />
low shrinking properties has been prepared by blending the acrylic<br />
syrup with a thermoplastic acrylic resin powder, which is poorly soluble<br />
in the syrup. The acrylic syrup consists essentially of methyl methacrylate<br />
or a (meth)acrylic monomer mixture <strong>and</strong> poly(methyl methacrylate) or an<br />
acrylic copolymer.<br />
To impart strength, solvent resistance, <strong>and</strong> dimension stability to a<br />
molded article, instead of pure methyl methacrylate monomer, a polyfunctional<br />
(meth)acrylic monomer may be added. It is preferable to replace<br />
the methyl methacrylate monomer by neopentyl glycol dimethacrylate up<br />
to 50%, since the molded article then has a remarkably excellent surface<br />
gloss. 24 The acrylic syrup may be obtained by dissolving the component<br />
acrylic polymer in the monomer, or a syrup can be obtained by partial<br />
polymerization of the component in the monomer.<br />
To the premix curing agents, such as dibenzoyl peroxide, lauroyl<br />
peroxide, tert-butyl hydroperoxide, cyclohexanone peroxide, methylethylketone<br />
peroxide, tert-butylperoxyoctoate, tert-butylperoxybenzoate,<br />
dicumyl peroxide, 1,1-bis(tert-butylperoxy)-3,3,5-trimethylcyclohexane,<br />
2,2 ′ -azobis(isobutyronitrile) are added. The filler then is added <strong>and</strong><br />
heat <strong>and</strong> pressure curing takes place for 10 minutes under conditions of<br />
a mold temperature of 130°C <strong>and</strong> a pressure of 100 kg/cm 2 to obtain an<br />
acrylic artificial marble with a thickness of 10 mm.<br />
9.6.2 Protective Coatings in Electronic Devices<br />
In semiconductor devices including a ferroelectric film or a dielectric film<br />
with a high dielectric constant, a surface coating has been proposed. This<br />
coating is made of an acrylic resin which prevents the degradation of the<br />
polarization properties of the ferroelectric or a film with a high dielectric<br />
constant, respectively, on the semiconductor device. 25
Acrylic Resins 363<br />
9.6.3 High-performance Biocomposite<br />
An environmentally friendly acrylic resin has been examined with respect<br />
to a high-performance biocomposite. Parameters such as the onset of curing<br />
reaction, the degree of cure at certain temperatures, <strong>and</strong> the swelling<br />
equilibrium data were analyzed. The crosslinking density after curing the<br />
resin at 180°C for 10 min indicates the completion of curing to a major<br />
extent under those conditions. 26<br />
9.6.4 Solid Polymer Electrolytes<br />
In conventional batteries with electrolytic solutions, the possible leakage<br />
of the electrolyte solution or elution of the electrode substance outside the<br />
battery presents a problem in long-term reliability. Batteries <strong>and</strong> electric<br />
double-layer capacitors using a solid polymer electrolyte are free of these<br />
problems. Also, these can be easily reduced in thickness.<br />
For installing a solid polymer electrolyte into a battery or electric<br />
double-layer capacitor, a method of using an electrolyte <strong>and</strong> a trifunctional<br />
methacrylic compound as the main components for the solid polymer electrolyte<br />
has been developed. The monomer for the solid polymer electrolyte<br />
is prepared from 2-isocyanatoethyl methacrylate <strong>and</strong> a branched oligo<br />
glycol. Such a glycol can be prepared by the etherification of glycerol,<br />
ethylene glycol, <strong>and</strong> propylene glycol. The isocyanate group adds with the<br />
pendent hydroxyl groups resulting in a trifunctional methacrylate ester. 10<br />
The synthesis is shown in Figure 9.6. Also, a mixture of poly(ethylene glycol)dimethacrylate<br />
<strong>and</strong> methoxypoly(ethylene glycol) mono methacrylate<br />
can serve as a monomer for solid polyelectrolyte polymers. 27<br />
It is desirable for a three-dimensional network structure to be<br />
formed. The polymerization is initiated by conventional peroxides or azo<br />
compounds. The whole formulation for a battery consists of:<br />
1. Methacrylic monomer,<br />
2. Polymerization initiator,<br />
3. Polymerization retarder,<br />
4. Electrolyte salt,<br />
5. Organic solvent, <strong>and</strong><br />
6. Inorganic particles.<br />
The process for manufacturing a complete battery is described in detail<br />
elsewhere. 10
364 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
CH 2<br />
CH 3<br />
CH C<br />
O CH 2 CH 2 NCO<br />
HOR<br />
CH 2<br />
CH 2<br />
CH 3<br />
CH C<br />
O CH 2 CH 2 NCO<br />
HOR<br />
CH<br />
O<br />
CH 2<br />
CH 3<br />
CH C<br />
O CH 2 CH 2 NCO<br />
HOR<br />
CH 2<br />
O<br />
O<br />
CH 2<br />
CH 3<br />
CH C<br />
O CH 2 CH 2 N C<br />
OR<br />
CH 2<br />
H<br />
O<br />
CH 3<br />
O<br />
H<br />
O<br />
CH 2<br />
CH<br />
C<br />
O<br />
CH 2<br />
CH 2<br />
N<br />
C<br />
OR<br />
CH<br />
CH 2<br />
CH 3<br />
CH C<br />
O CH 2 CH 2 N C<br />
OR<br />
CH 2<br />
O<br />
H<br />
O<br />
O<br />
R = (CH 2 CH 2 O) n (CH 2 CHO) m<br />
CH 3<br />
Figure 9.6: Synthesis of a Methacrylate Monomer for a Solid Electrolyte 10
Acrylic Resins 365<br />
9.7 SPECIAL FORMULATIONS<br />
9.7.1 Silane <strong>and</strong> Siloxane Acrylate Resins<br />
Weather resistant resin coatings can be prepared by an addition polymerization<br />
reaction of n-butyl acrylate, methyl methacrylate, n-butyl<br />
methacrylate, <strong>and</strong> 3-methacryloxypropyl-trimethoxysilane (MPTS). The<br />
weather resistant silicone/acrylic resin coatings are then blended with<br />
TiO 2 . The viscosity of the resin decreases with increasing content of<br />
MPTS, whereas the thermal stability at high temperature increases.<br />
5, 28, 29<br />
Coatings with 30% MPTS have especially good weather resistant properties.<br />
UV-curable formulations for UV-transparent optical fiber coatings<br />
have been developed. Poly(dimethylsiloxane-acrylate) resins showed the<br />
best performance with respect to the monomer reactivity <strong>and</strong> the UV-transparency<br />
of the polymer coating. An acyl-phosphine oxide proved to be<br />
the best suited because of its high reactivity, fast photolysis, <strong>and</strong> lack of<br />
absorbing of the by-products of photo curing at the wavelength of operation.<br />
21<br />
9.7.2 Marble Conservation<br />
Marble <strong>and</strong> stone used as building materials are susceptible to environmental<br />
damage. Acrylic resins can be used as carriers of suitable pigments for<br />
the protection of the surface of a monument. Copolymers of ethyl methacrylate<br />
<strong>and</strong> methyl acrylate have been extensively applied as a protective<br />
agent for stone building materials since the 1950s.<br />
The photodegradation of acrylic resins containing titanium dioxide<br />
pigments has been studied under UV irradiation. Two kinds of TiO 2 ,<br />
anatase <strong>and</strong> a mixture of anatase <strong>and</strong> rutile, were used in different concentrations.<br />
The changes caused by the irradiation treatment were monitored<br />
by Fourier transform infrared spectroscopy, gel permeation chromatography,<br />
<strong>and</strong> solubility measurements. The presence of anatase pigment<br />
significantly improved the photostability. 30 Films of acrylic resins of varying<br />
compositions were applied both on a dolomitic white marble support<br />
<strong>and</strong> on potassium bromide disks <strong>and</strong> exposed to UV light. The main degradation<br />
pathway under ultraviolet irradiation is the chain scission. The rates<br />
of photodegradation may be related to the type of ester group <strong>and</strong> to the<br />
presence of the α-methyl group in the main chain. 31
366 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Blends of acrylic resins <strong>and</strong> fluoroelastomer are also suitable materials<br />
in stone protection. Films of a copolymer of ethyl methacrylate<br />
<strong>and</strong> methyl acrylate blended with a copolymer of vinylidene fluoride <strong>and</strong><br />
hexafluoropropene were investigated by means of FT-IR spectroscopy <strong>and</strong><br />
FT-IR microspectroscopy before <strong>and</strong> after UV <strong>and</strong> thermal treatments. A<br />
high content of fluoroelastomer increases the stability of these blends. A<br />
solution of a blend described above in tetrahydrofuran was successfully applied<br />
to a marble surface of the Saint Maria Cathedral in Lucca, Toscana. 32<br />
9.7.2.1 Degradation by Lipase<br />
Layers of an aged acrylic resin, a fifteenth-century tempera painting on<br />
panel <strong>and</strong> a nineteenth-century oil painting on canvas have been removed<br />
by the action of lipases. Lipases are hydrolytic enzymes that act on glycerol<br />
ester bonds. These enzymes are a less aggressive alternative to highly polar<br />
organic solvents or alkaline mixtures. 33<br />
9.7.3 Tackifier Resins<br />
Acrylic resins are suitable as tackifier resins in pressure-sensitive adhesive<br />
applications. They can be prepared by free-radical polymerization. The<br />
acrylic tackifier is then blended with a natural rubber base in various ratios.<br />
Investigation of the mechanical properties showed that blends with a good<br />
pressure-sensitive adhesive performance have a higher loss of tangent-δ at<br />
higher frequencies. 34<br />
9.7.4 Drug Release Membranes<br />
The feasibility of a transdermal delivery system (TDS) for 17-β-estradiol<br />
was investigated by in vitro release studies. Unilaminate adhesive devices<br />
capable of releasing 17-β-estradiol in a controlled fashion over a period up<br />
to 216 hours have been developed using acrylic resins. The release of drug<br />
from the adhesive devices seems to obey a zero-order kinetics.<br />
Acetyltributyl citrate (ATBC), triethyl citrate (TEC), propylene glycol<br />
(PG) <strong>and</strong> myristic acid (MA) are plasticizers that can modify the release<br />
patterns of the drug. The study demonstrated that the acrylic resins<br />
are suitable polymers for the preparation of 17-β-estradiol TDS adhesive<br />
devices. 35
Acrylic Resins 367<br />
9.7.5 Support Materials for Catalysts<br />
Palladium-tin catalysts can be deposited on acrylic resins bearing carboxylic<br />
functional groups. The resins act as support materials for the catalysts.<br />
The catalysts are suitable for the selective hydrogenation of 100 ppm aqueous<br />
nitrate solutions. The materials exhibit different Sn contents <strong>and</strong> show<br />
different reduction temperatures.<br />
A high COOH content in the support is important in the control of<br />
the selectivity of the catalysts limiting ammonia formation. 36<br />
Copper ion catalysts can be immobilized on acrylic resins (rather<br />
than acrylonitrile resins) with aminoguanidyl groups. They are prepared<br />
by modification of the nitrile groups in an acrylonitrile, vinyl acetate, <strong>and</strong><br />
divinylbenzene terpolymer using aminoguanidine carbonate.<br />
The catalysts act on the oxidation of hydroquinone to p-benzoquinone<br />
with hydrogen peroxide as oxidant. The catalytic activity <strong>and</strong> selectivity<br />
in the Cu(II)-resin system increases in comparison to the reaction<br />
without a catalyst <strong>and</strong> the reaction with native Cu(II) ions. 37<br />
9.7.6 Electron Microscopy<br />
Acrylic resins can be used for low-temperature embedding of samples in<br />
electron microscopy. 38<br />
9.7.7 Stereolithography<br />
Three-dimensional objects can be built without the use of molds by stereolithography.<br />
The objects are obtained layer by layer by polymerizing a<br />
low-viscosity liquid resin under a laser beam. The kinetic behavior of the<br />
resin is essential for a complete curing which occurs in the small zone<br />
exposed to laser irradiation.<br />
The isothermal kinetic behavior of a commercial acrylic resin for<br />
stereolithography has been analyzed by differential photocalorimetric analysis.<br />
A kinetic model accounting for the effect of autoacceleration, the<br />
vitrification, <strong>and</strong> light intensity has been set up. 39<br />
9.7.8 Laminated Films<br />
Laminated films of acrylic resins are constituted of a soft layer formed of<br />
an acrylic resin with rubber particles incorporated <strong>and</strong> a hard layer also<br />
formed of an acrylic resin.
368 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
By incorporating rubber particles into an acrylic resin, the flexibility<br />
is improved while all other positive properties, such as transparency <strong>and</strong><br />
surface gloss, are maintained. To have a hard outer surface two films, one<br />
of them filled with rubber particles <strong>and</strong> one being unfilled, are combined.<br />
The laminated film is excellent in surface hardness, flexibility <strong>and</strong><br />
ability to prevent whitening from occurring during molding or forming <strong>and</strong><br />
hence is suitable for use as a surface material for moldings, such as interior<br />
materials for vehicles, exterior materials for household electrical appliances<br />
<strong>and</strong> building materials (exterior), which are obtained by a molding<br />
or forming process requiring bending or stretching. 12<br />
9.7.9 Ink-jet Printing Media<br />
An ink-jet printing system is one wherein ink droplets are jetted onto a<br />
surface of a printing medium <strong>and</strong> attached thereon.<br />
Therefore, the surface of the printing medium needs to rapidly absorb<br />
the jetted ink droplets. The printing media for use in the ink-jet printing<br />
system are not limited to paper but include various materials such as<br />
transparent resin films for overhead films <strong>and</strong> metals. Some of these printing<br />
media have no hydrophilic surfaces. Therefore, in order to clearly print<br />
information, an ink-receiving layer needs to be provided on the surface of<br />
a substrate constituting the printing medium. The ink-jet printing media<br />
are required to have the following characteristics:<br />
• Permeation of ink inside the ink-receiving layer must be rapidly<br />
made, color running should not take place, <strong>and</strong> clear color having<br />
high chromaticity can be reproduced.<br />
• In the multi-color printing using a combination of ink components,<br />
each ink component must be rapidly absorbed even if ink dots are<br />
superposed on the same surface of the printing medium, <strong>and</strong> in the<br />
high-speed printing, the printed surface must be free from staining,<br />
<strong>and</strong> the ink absorption rate <strong>and</strong> the ink absorption quantity both<br />
must be satisfactory.<br />
• The printing medium must have water resistance, <strong>and</strong> even if the<br />
printed image is contacted by water, running or bleeding of ink of<br />
the image must not take place.<br />
• Even if the ink-jet printing media are stored in the superposed<br />
state, they must be free from blocking.
Acrylic Resins 369<br />
• Even if the printed matter is stored for a long period of time, color<br />
fading should not take place.<br />
Proposals for forming an ink-receiving layer containing hydrophilic<br />
resins include 40<br />
• Starch <strong>and</strong> other water-soluble cellulose derivatives,<br />
• Polyvinyl alcohol, modified polyvinyl alcohol,<br />
• Polyvinyl pyrrolidone,<br />
• Polyvinyl acetal, <strong>and</strong><br />
• Hydrophilic acrylic copolymer having a crosslinked structure on<br />
the substrate surface.<br />
A hydrophilic acrylic copolymer having a crosslinked structure consists<br />
of acrylamide, methacrylamide <strong>and</strong> other amides, acrylic acid <strong>and</strong><br />
acrylic esters, such as glycidyl acrylate <strong>and</strong> the corresponding methacrylate<br />
derivatives, respectively. Examples of crosslinking agents include divinylbenzene,<br />
ethylene glycol acrylate, <strong>and</strong> triethylene glycol diacrylate. A suitable<br />
polymerization initiator is 2,2 ′ -azobis(2-amidinopropane)hydrochloride<br />
or dibenzoyl peroxide in toluene. The polymerization is carried out<br />
in aqueous isopropyl alcohol <strong>and</strong> poly(oxyethylene) nonylphenyl ether. 40<br />
The copolymer was isolated <strong>and</strong> a dispersion was prepared that was applied<br />
on wood-free paper <strong>and</strong> poly(ethylene terephthalate).<br />
REFERENCES<br />
1. J. W. Nemec <strong>and</strong> W. Bauer. Acrylic <strong>and</strong> methacrylic ester polymers. In<br />
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5. H. S. Park, D. J. Chung, H. S. Hahm, S. K. Kim, W. B. Im, <strong>and</strong> S. J. Kim.<br />
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coatings. J. Chem. Eng. Jpn., 37(2):158–165, February 2004.<br />
6. H. Nomura, Y. Kimata, H. Kanai, Y. Yokota, <strong>and</strong> M. Yoshida. Weatherability<br />
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Iron Steel Inst. Jpn., 89(1):128–134, January 2003.<br />
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11. B. W. L. Jang, M. R. Gogate, J. J. Spivey, J. R. Zoeller, R. D. Colberg, <strong>and</strong><br />
G. N. Choi. Synthesis of methyl methacrylate from coal-derived syngas. US<br />
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12. K. Koyama <strong>and</strong> Y. Tadokoro. Acrylic resin laminated film <strong>and</strong> laminated<br />
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13. S. Tayama <strong>and</strong> N. Kusakawa. Flame resistant acrylic resin composition<br />
<strong>and</strong> process for its production. US Patent 4 533 689, assigned to Mitsubishi<br />
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14. F. Sawaragi <strong>and</strong> H. Sonezaki. Abrasion-resistant coating composition for<br />
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20. C. D. Diakoumakos, Q. Xu, F. N. Jones, J. Baghdachi, <strong>and</strong> L. M. Wu. Synthesis<br />
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polymerization. J. Coat. Technol., 72(908):61–70, September 2000.<br />
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49(1):1–12, January 2004.<br />
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24. Y. Ikegami, S. Koyanagi, Y. Kishimoto, <strong>and</strong> Y. Nakahara. Acrylic resin composition,<br />
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32. E. Benedetti, A. D’ Alessio, M. F. Zini, E. Bramanti, N. Tirelli, P. Vergamini,<br />
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10<br />
Cyanate Ester Resins<br />
Cyanate ester resins are a comparatively new generation of thermosetting<br />
resins. They are characterized by the cyanate group as a reactive group.<br />
Most materials of this class are aromatic. Cyanate esters exhibit attractive<br />
physical, electrical, thermal, <strong>and</strong> processing properties. Blends with epoxy<br />
<strong>and</strong> bismaleimide are common. Major applications are in microelectronics,<br />
aerospace, <strong>and</strong> related areas. 1–3<br />
10.1 HISTORY<br />
Cyanate chemistry was discovered in 1964. Cyanate ester resins have been<br />
commercialized since the late 1970s.<br />
10.2 MONOMERS<br />
Cyanate esters bear basically two cyanate groups (-OCN) attached to an<br />
aromatic ring. Also aryl cyanate esters with additional allyl groups are<br />
known, e.g., 1-allyl-2-cyanatobenzene. Allyl-modified types act as reactive<br />
diluents in combination with bismaleimide resins.<br />
10.2.1 Specialities<br />
Modifications in the thermal <strong>and</strong> mechanical properties are achieved by<br />
blending cyanate esters with epoxies. This is used in particular for adjust-<br />
373
374 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
ing the tack, drape flow, <strong>and</strong> other rheological properties. Functionalized<br />
thermoplastic oligomers can be also used for modification.<br />
10.2.1.1 Monofunctional Cyanates<br />
Monofunctional cyanates such as dinonylphenol cyanate can be used to<br />
modify a fluorinated bisphenol A dicyanate monomer. The monofunctional<br />
cyanate reduces the crosslink density in the cured network. Long network<br />
chains between the branching points can be prepared by polymeric endcapped<br />
dicyanates.<br />
10.2.1.2 Alkenyl-modified Resins<br />
Cyanate ester monomers, functionalized with alkenyl groups, raise the<br />
glass transition temperature when used in conjunction with bismaleimide<br />
resins. 4 Alkenyl groups are addressed as reactive modifiers because they<br />
have the ability to react with both homopolymers (cyanate ester <strong>and</strong> bismaleimide)<br />
to form networks.<br />
10.2.1.3 Low-dielectric Cyanates<br />
Fluoroaliphatic Cyanates. Fluoroaliphatic cyanates can be prepared from<br />
a fluoro methylol precursor, such as HOCH 2 (CF 2 ) 6 CH 2 OH, <strong>and</strong> cyanogen<br />
bromide. A solution of cyanogen bromide is reacted with a fluoromethylol<br />
precursor with triethylamine as catalyst at −20°C. The product is recovered<br />
by dilution with a water-immiscible organic solvent, extraction with water,<br />
separation, drying, <strong>and</strong> concentration of the organic phase. 5<br />
Resins from such materials have a very low permittivity to electric<br />
fields, as needed for improving the performance in microelectronics. The<br />
length of the fluoromethylene chain correlates with decreasing dielectric<br />
constant, decreasing moisture absorption, <strong>and</strong> increasing thermal stability.<br />
In general, fluoroaliphatic cyanate resins have dielectric constants in the<br />
range of 2.3 to 2.6, tanδ loss lower than 0.02, <strong>and</strong> a low moisture absorption.<br />
o-Methylated Cyanates. The ortho-methylation of a bis(4-cyanatocumyl)-<br />
benzene cyanate ester showed a further decrease of the dielectric constant.<br />
However, other physical properties are also affected. The glass transition
Cyanate Ester Resins 375<br />
OH + Cl C N<br />
- HCl<br />
O C N<br />
H 2 O<br />
O<br />
O C NH 2<br />
Figure 10.1: Formation of Cyanates, Hydrolysis with Water to a Carbamide (not<br />
desired)<br />
temperature decreases by 40°C <strong>and</strong> the coefficient of thermal expansion<br />
increases; thermal stability is reduced. 6<br />
10.2.2 Synthesis<br />
Cyanates are formed by the reaction of phenols with cyanogen halides. The<br />
reaction is shown in Figure 10.1. A tertiary amine is catalytically active.<br />
The reaction is sensitive to traces of water. Water hydrolyzes aryl cyanates<br />
into carbamates. On the other h<strong>and</strong>, if the condensation is conducted at<br />
temperatures near 0°C, the water seems not to affect the reaction. 7 Low<br />
boiling esters can be purified by distillation. The impurities can be reduced<br />
by proper selection of the solvent used in crystallization <strong>and</strong> washing steps<br />
after the synthesis of the cyanate ester. Polymeric cyanate esters can be<br />
purified by repeated precipitation processes.<br />
The synthesis of various bisphenol dicyanate monomers has been reported.<br />
Several cyanate esters are commercially available. Monomers for<br />
cyanate ester resins are listed in Table 10.1 <strong>and</strong> shown in Figure 10.2. Most<br />
of the monomers are based on bisphenols. Other cyanates are obtained by
376 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
NCO<br />
CH 3<br />
C<br />
OCN<br />
CH 3<br />
2,2-Bis(4-cyanatophenyl)propane<br />
CH 3<br />
NCO<br />
C<br />
OCN<br />
H<br />
1,1-Bis(4-cyanatophenyl)ethane<br />
H 3 C<br />
CH 3<br />
H<br />
NCO<br />
C<br />
OCN<br />
H<br />
H 3 C<br />
CH 3<br />
Bis(3,5-dimethyl-4-cyanatophenyl)methane<br />
NCO<br />
S<br />
OCN<br />
Bis(4-cyanatophenyl)thioether<br />
NCO<br />
CH 3<br />
C<br />
NCO<br />
C CH CH 3<br />
CH 3<br />
CH 3<br />
3<br />
C<br />
CH 3<br />
1,3-Bis(4-cyanatophenyl-1-(methylethylidene))benzene<br />
Figure 10.2: Bisphenol-based Cyanate Esters
Compound<br />
Table 10.1: Monomers<br />
Cyanate Ester Resins 377<br />
Remark/Reference<br />
2,2-Bis(4-cyanatophenyl)propane AroCy B-10<br />
1,1-Bis(4-cyanatophenyl)ethane AroCy L-10<br />
Bis(4-cyanatophenyl)methane<br />
Bis(3,5-dimethyl-4-cyanatophenyl)methane<br />
1,3-Bis(4-cyanatophenyl-1-(methylethylidene))benzene<br />
Bis(4-cyanatophenyl)thioether<br />
7<br />
Bis(4-cyanatophenyl)ether<br />
1,3-Bis(4-cyanatophenyl-1-(1-methylethylidene))benzene XU 366<br />
1,1-Dibromo-2,2-bis(4-cyanatophenyl)ethylene<br />
8 a<br />
1,1-Dichloro-2,2-bis(4-cyanatophenyl)ethylene<br />
8 a<br />
2,2-Bis(4-Cyanatophenyl)1,1,1,3,3,3-hexafluoropropane<br />
4,4-Dicyanatobiphenyl<br />
Resorcinol dicyanate<br />
2,7-dihydroxynaphthalene dicyanate<br />
9<br />
1,1-bis(3-methyl-4-cyanatophenyl)cyclohexane<br />
10<br />
a Flame Retardant<br />
reactions of novolak <strong>and</strong> cyan halides. 11 The carbon atom in the cyanato<br />
group is highly electrophilic. It is therefore prone to a nucleophilic reagent<br />
attack.<br />
10.3 SPECIAL ADDITIVES<br />
10.3.1 Fillers<br />
10.3.1.1 Silica<br />
In semiconductor encapsulation, a large amount of inorganic filler, typically<br />
65% is used. As is the case of epoxy based encapsulants, <strong>and</strong> also in<br />
cyanate ester composites, a silica filler increases the conductivity, Young’s<br />
modulus, <strong>and</strong> dielectric constant. The filler decreases the thermal expansion.<br />
A high degree of interfacial adhesion between the untreated silica<br />
filler <strong>and</strong> the cyanate ester matrix is obtained. 12<br />
10.3.1.2 Silicate Nanocomposites<br />
Nanocomposites improve the properties of cyanate resins. 13 The addition<br />
of silicate nanocomposites increases the onset of the thermal decompo-
378 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
sition. The glass transition temperature T g increases from 354°C for the<br />
neat resin, to 387°C for a 2.5% loading with nanocomposites. The fracture<br />
toughness <strong>and</strong> the flexural modulus increase by 30% with a loading of 5%.<br />
10.3.2 Flame Retardants<br />
In general, cyanate ester resins exhibit a better flame retardancy than epoxy<br />
resins. In electronic applications, laminates are generally required to<br />
possess a wide range of favorable properties, including high mechanical<br />
strength, good thermal stability, good chemical resistance, low heat distortion,<br />
a high resistance to aging, good electric insulation properties, consistent<br />
dimensional stability over a wide temperature range, good adhesion to<br />
glass <strong>and</strong> copper, a high surface resistivity, a low dielectric constant <strong>and</strong><br />
loss factor, ease of drillability, low water absorption, <strong>and</strong> a high corrosion<br />
resistance. Additionally or even equally important is the limited flammability.<br />
Epoxy resins alone or in combinations with cyanate esters or other<br />
additives, which are widely used in the electronic industry for printed circuit<br />
board (PCB) laminate applications, meet these requirements only because<br />
they contain approximately 30 to 40% brominated aromatic epoxy<br />
components. This is 17% to 32% as elemental bromine.<br />
Antimony <strong>and</strong> halogen compounds have been added to resins in order<br />
to impart flame retardancy. The problem with these brominated compounds<br />
is that, although they have excellent flame-retardant properties,<br />
they also have some undesirable properties. The chemical decomposition<br />
of aromatic bromine compounds releases free bromine radicals <strong>and</strong> hydrogen<br />
bromide, which are highly corrosive. Additionally, when highly<br />
brominated aromatics decompose in the presence of oxygen, they may<br />
form the highly toxic brominated dibenzofurans as some past studies have<br />
shown. Consequently, interest in displacing the use of brominated aromatic<br />
epoxies emerged.<br />
Fillers with an extinguishing flame effect, such as antimony trioxide,<br />
aluminum oxide hydrates, aluminum carbonates, magnesium hydroxides,<br />
borates, <strong>and</strong> phosphates, have been proposed for the replacement of brominated<br />
aromatics. However, all these fillers have the disadvantage that they<br />
often seriously impair the mechanical, chemical, <strong>and</strong> electrical properties<br />
of the laminates. In the case of antimony trioxide, it is listed as a carcinogen.
Cyanate Ester Resins 379<br />
The flame-retardant effect of red phosphorus has also been investigated<br />
in some cases combined with finely divided silicon dioxide or aluminum<br />
oxide hydrate. Such compositions when used in electronic applications<br />
may lead to corrosion due to the formation of phosphoric acid in the<br />
presence of moisture.<br />
In addition, organic phosphorus compounds, such as phosphoric acid<br />
esters, phosphonic acid esters <strong>and</strong> phosphines, were proposed as flame-retardant<br />
additives. These alternatives have not been promising due to plasticization<br />
effects that they impart to the base resin. Other useful phosphorus-containing<br />
compounds include propanephosphonic anhydride, <strong>and</strong><br />
ethylmethylphosphinic anhydride. 14 These flame retardants are allowed<br />
to react with the epoxide component. Monomers with the phenylphosphine<br />
oxide structure exhibit good thermooxidative properties <strong>and</strong> increased<br />
yields of char when heated.<br />
10.4 CURING<br />
Essentially no volatile by-products are formed in the course of curing.<br />
Many cyanate esters do not shrink during cure.<br />
10.4.1 Thermal Curing<br />
Cyanate ester resins are polymerized by a cyclotrimerization of the cyanato<br />
functions. The cyclotrimerization produces aryloxytriazine rings which<br />
serve as the crosslink sites in the final thermoset matrix. The cyclotrimerization<br />
is shown in Figure 10.3. Very high temperatures, beyond 300°C, are<br />
usually required for the crosslinking by cyclotrimerisation of cyanate ester<br />
groups in uncatalyzed systems. 15 However, suitable catalysts are available<br />
<strong>and</strong> usually catalysts are added. Then, the triazine rings are formed around<br />
180°C. 16 In fact, the mechanism of cyclotrimerization is much more complicated.<br />
17 Analysis of the initial products of curing by gel permeation<br />
chromatography indicates that the dimer is a straight chain with a primary<br />
amino group. The triazine ring in the trimers seems to exert a strong catalytic<br />
effect on the remaining cyanate groups so that the reactivity from the<br />
stage of trimers is significantly increased. The reactivities of the higher<br />
intermediates decrease up to the heptamer. The monomer consumption in<br />
the initial stage of curing follows a second-order rate kinetics. 18 In the<br />
case of a novolak-type cyanate ester monomer, an autocatalytic behavior
380 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
C<br />
N<br />
N<br />
C<br />
O<br />
C<br />
N<br />
O<br />
O<br />
N<br />
O<br />
N<br />
N<br />
O<br />
Figure 10.3: Cyclotrimerization of Cyanate Esters
Compound<br />
Table 10.2: Curing Agents<br />
Cyanate Ester Resins 381<br />
Reference<br />
Zinc octoate<br />
Bis(1-methyl-imidazole)zinc(II)dicyanate<br />
19<br />
Bis(1-methyl-imidazole)zinc(II)dioctoate<br />
Bis(1-methyl-imidazole)zinc(II)diacetyl-acetonate<br />
Aluminium(III)acetylacetonate <strong>and</strong> dodecylphenol<br />
20<br />
Cobalt(II)acetylacetonate <strong>and</strong> nonylphenol<br />
21<br />
Dibutyltin dilaurate<br />
22<br />
2,2 ′ -Diallyl bisphenol A (DBA)<br />
15<br />
was observed. 23 The same is true for epoxy blends. 24<br />
Various techniques for monitoring the curing of a bisphenol A dicyanate<br />
ester resin have been screened, including UV, fluorescence, phosphorescence,<br />
<strong>and</strong> IR techniques. During curing, a very strong luminescence<br />
emission has been found.<br />
The fluorescence emission intensity around 420 nm first increases<br />
followed by a decrease with a small red shift as the cure reaction proceeds.<br />
The aromatically substituted cyanurates formed during curing exhibit an<br />
inner filter effect <strong>and</strong> are thus responsible for the observed emission <strong>and</strong> its<br />
trend in intensity. 25<br />
As catalysts, Lewis acids <strong>and</strong> carboxylic salts of transition metal are<br />
suitable. For example, zinc naphthenate <strong>and</strong> nonylphenol cure the ester at<br />
149°C. Further catalysts are given in Table 10.2. Besides trimerization, the<br />
formation of dimers <strong>and</strong> higher oligomers was observed in small amounts.<br />
Aryl cyanates are converted cleanly at 25°C to 1,3,5-triazines by<br />
catalytic amounts of titanium tetrachloride in dichloromethane. A mechanism<br />
has been proposed involving a rate-limiting nucleophilic attack of the<br />
cyanate nitrogen on the cyanato carbon of a cyanate-titanium tetrachloride<br />
complex. The subsequent steps are fast. 26<br />
10.4.2 Curing with Epoxy Groups<br />
Curing by the reaction with epoxy groups is also possible. The reaction is<br />
shown in Figure 10.4. The reaction is proposed to run via an intermediate<br />
trimer of the cyanate ester. The epoxy component acts as a toughener for<br />
cyanate ester resins.<br />
The chemical structure of the cyanate monomer can affect the cur-
382 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O C N<br />
CH 2<br />
+<br />
O<br />
CH<br />
O<br />
C<br />
N<br />
O<br />
Figure 10.4: Reaction of Cyanate Esters with an Epoxide to Produce an Oxazoline<br />
Structure<br />
ing reactions <strong>and</strong> thermal properties of the final product. In a comparative<br />
study, 2,2 ′ -bis(4-cyanatophenyl)propane was blended <strong>and</strong> cured with epoxy<br />
based bisphenol or tetramethyl bisphenol.<br />
The oxazolidinone ring structure is dominant when curing the bisphenol<br />
epoxy system, whereas a cyanurate ring is predominant in the curing<br />
reaction of a tetramethyl bisphenol epoxy system. This is attributed to<br />
the bulky methyl groups. The crosslinked cyanurate structure has a higher<br />
thermal stability than the linear oxazolidinone structure. 27<br />
In epoxy/dicyanate blends containing an amine curing agent, the<br />
cure rate increases with increasing dicyanate content. The reaction mechanism<br />
is autocatalytic <strong>and</strong> is second-order. 24<br />
10.4.3 Curing with Unsaturated Compounds<br />
Figure 10.5 shows the reaction of cyanate esters with unsaturated compounds,<br />
exemplified with a maleimide <strong>and</strong> an acetylenic compound. Phenolic<br />
hydroxy groups have a catalytic effect on the cyclotrimerisation of<br />
cyanate esters. 2,2 ′ -Diallyl bisphenol A (DBA), with two phenolic hydroxy<br />
groups, has been used as a catalyst for the crosslinking of a cyanate<br />
ester (CE). The double bonds on DBA can readily copolymerize with bismaleimide<br />
to form an interpenetrating polymer network (IPN). 15 This type<br />
of resin system is addressed as self-catalytic. The crosslinks are formed by<br />
different reactions. By such a combination, cyanate esters can be cured<br />
at a lower temperature while largely maintaining their superior dielectric<br />
properties.
Cyanate Ester Resins 383<br />
O<br />
R<br />
N<br />
O<br />
O<br />
N<br />
N<br />
O<br />
O<br />
R<br />
N<br />
O<br />
O C N N C O<br />
R<br />
C<br />
C<br />
R<br />
O<br />
N<br />
O<br />
N<br />
R<br />
R<br />
Figure 10.5: Reaction of Cyanate Esters with Unsaturated Compounds
384 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
However, these resins exhibit somewhat lower mechanical properties.<br />
The flexural strength, flexural strain at break, <strong>and</strong> impact strength of<br />
the BMI/DBA-CE IPN cured resin systems are relatively lower than that<br />
calculated by the rule of mixtures, i.e., BMI/DBA <strong>and</strong> CE. 28<br />
10.4.4 Initiator Systems<br />
10.4.4.1 Encapsulated Initiators<br />
To combine properties such as long pot life, short cure time, <strong>and</strong> high glass<br />
transition temperature, small particles of effective hardeners were encapsulated<br />
to make them insoluble <strong>and</strong> nonreactive when mixed with the resin<br />
at room temperature. By this technique, pot lifes of more than 3 months<br />
could be reached, whereas the same cyanate ester gels <strong>and</strong> becomes solid<br />
within 30 min at the room temperature, if a neat hardener is used instead<br />
of the capsules.<br />
However, on heating, the capsules open <strong>and</strong> the curing reaction starts<br />
immediately. Low-temperature systems with cure times less than 5 min<br />
at 80°C can reach glass temperatures of about 140°C. A glass transition<br />
temperature of 220°C after only 10 sec curing time can be achieved with<br />
certain formulations. Such systems are also addressed as snap cure resin<br />
systems. They can be easily mixed with a lot of common additives such as<br />
minerals, tougheners, metallic powders, <strong>and</strong> others to cover a wide range<br />
of performance characteristics. 29<br />
10.4.4.2 Photoinitiators<br />
Cyanate esters can be rendered photosensitive by mixing with a cationic<br />
photoinitiator. Photosensitive compositions containing cyanate esters can<br />
be used as permanently retained etch masks, solder masks, plating masks,<br />
dielectric films, <strong>and</strong> protective coatings. The cured products can withst<strong>and</strong><br />
temperatures up to 360°C. The materials, depending upon the type of photoinitiator<br />
selected, can be used as both positive <strong>and</strong> negative resists.<br />
Suitable photoinitiators are arylacyldialkyl <strong>and</strong> hydroxyaryldialkyl<br />
sulfonium salts. When a negative working photoresist is desired, the photoinitiator<br />
employed is one which will generate a Lewis acid upon exposure<br />
to actinic light. Examples of such photoinitiators are iron arenes. Furthermore,<br />
photosensitizers can be added. Suitable photosensitizers include perylene(peri-dinaphthalene),<br />
anthracene derivatives (e.g., 9-methylanthrac-
Cyanate Ester Resins 385<br />
ene), dyes (e.g., acridine orange, acridine yellow, benzoflavin), <strong>and</strong> titanium<br />
dioxide. 30 Modified resins, containing epoxy acrylate, a cyanate ester<br />
compound, <strong>and</strong> an anhydride are used. 11<br />
10.5 PROPERTIES<br />
Cyanate monomers have a low toxicity with an LD 50 of 3 g/kg. 31 Cyanate<br />
ester resins are superior to epoxy resins, phenolic resins, <strong>and</strong> bismaleimide<br />
resins. They combine the advantages of epoxies, the fire resistance<br />
of phenolics, <strong>and</strong> the high-temperature performance of polyimides. The<br />
crosslinked networks of cyanacrylate resins can exhibit a T g higher than<br />
300°C. They are thermally stable up to 475°C.<br />
A systematic study on the effect of silica fillers in an AroCy B cyanate<br />
ester polymer in the range from 15% to 70% on the thermal, mechanical,<br />
<strong>and</strong> conductivity properties has been presented. 12<br />
10.5.1 Modelling<br />
The prediction of the physical <strong>and</strong> mechanical properties of new potential<br />
poly(cyanurate)s prior to synthesis is an important issue for future technological<br />
application. Several important properties have been predicted by<br />
molecular dynamics programs. For example, the glass transition temperature<br />
(T g ) can be simulated by monitoring changes in cell volume while<br />
keeping the number of the atoms, the pressure, <strong>and</strong> the total energy constant.<br />
31 Also, the curing behavior under process conditions has been modelled.<br />
32<br />
10.6 APPLICATIONS AND USES<br />
10.6.1 Composites<br />
Dicyanates of bisphenol derivatives are currently used in composites with<br />
established reinforcements such as carbon fiber, glass fiber, silica cloth,<br />
<strong>and</strong> pitch-based graphite fibers.<br />
10.6.2 Electronic Industry<br />
Cyanate ester laminates are primarily used in the electronic industry for<br />
printed circuit boards. These laminates show a low dielectric constant, loss<br />
factor, <strong>and</strong> superior peel strength with respect to copper.
386 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
10.6.3 Spacecraft<br />
High-temperature composite solar array substrate panels for spacecraft applications<br />
to orbit the planet Mercury are made from pitch-fiber composite<br />
material containing cyanate ester resins. The thermal, mass <strong>and</strong> stiffness<br />
requirements suggested the panels should be fabricated from a high conductivity<br />
<strong>and</strong> stiffness pitch-fiber composite material capable of withst<strong>and</strong>ing<br />
short-term temperatures as high as 270°C. 33<br />
10.7 SPECIAL FORMULATIONS<br />
10.7.1 PT Resins<br />
To obviate certain disadvantages attendant to phenolic resins, a modified<br />
multifunctional phenolic cyanate/phenolic triazine copolymer (PT) has<br />
been developed. This resin type has greater oxidative, mechanical, <strong>and</strong><br />
thermal stability than conventional phenolic resins. Further, it did not produce<br />
volatile by-products during crosslinking. In addition, the PT resins<br />
possess better elongation properties <strong>and</strong> higher glass transition temperatures<br />
than the conventional phenolic resins. 34<br />
10.7.2 Blends with Epoxies<br />
Blending of cyanate esters with epoxy resins is one of the most important<br />
modifications. Most commercial cyanate ester prepregs are, in fact, made<br />
from cyanate ester/epoxy blends. During curing, a complicated reaction<br />
occurs in the blends. The cyanate resin can act here as a latent catalyst<br />
for the epoxy resin. 35 In blends, the following mechanisms of curing have<br />
been postulated:<br />
1. Polycyclotrimerization,<br />
2. Formation of oxazoline,<br />
3. Insertion of epoxy groups into cyanurate,<br />
4. Formation of tetrahydrooxazolooxazole, <strong>and</strong><br />
5. Ring cleavage <strong>and</strong> reformation of oxazoline.<br />
In dicyanate-novolak epoxy resin blends, most of the oxazolidinone<br />
is formed by isomerization of oxazoline rather than by insertion of epoxy<br />
into isocyanurate. 36 The moisture uptake of certain dicyanate-epoxy novolak<br />
blends is substantially lower than that of the homopolycyanate. 37
Cyanate Ester Resins 387<br />
Formulations made from bisphenol A cyanate ester <strong>and</strong> diglycidyl ether of<br />
bisphenol A epoxy resin, or o-cresol formaldehyde novolak epoxy resin,<br />
have enhanced processing characteristics. 38<br />
Resins of high crosslink density <strong>and</strong> high glass transition temperature<br />
appeared to exhibit a larger reduction in glass transition temperature<br />
upon plasticization by moisture compared to those with lower crosslink<br />
density. 39<br />
Epoxy backbones with hard-soft segments were tailored to improve<br />
the toughness. Epoxide <strong>and</strong> cyanate ester resins with isophthalic<br />
<strong>and</strong> terephthalic groups in the backbone, i.e., 1,3-[di(4-glycidyloxy diphenyl-2,2<br />
′ -propane)]isophthalate (DGDPI) <strong>and</strong> 1,4-[di(4-cyanato diphenyl-2,2<br />
′ -propane)]terephthalate (DCDPT) exhibit higher T g compared to a<br />
st<strong>and</strong>ard epoxy system. The increase in the T g is attributed to the cyanate<br />
ester <strong>and</strong> rigid aromatic backbones present.<br />
40, 41<br />
10.7.3 Bismaleimide Triazine Resins<br />
Bismaleimide triazine resins (BT) are used for high density circuit boards<br />
because of their good thermal stability. Bismaleimide triazine resins consist<br />
of bismaleimide, a cyanate ester, <strong>and</strong> epoxy compounds. 42 A BT resin<br />
can be cured with peroxide initiators, such as dicumyl peroxide or dibenzoyl<br />
peroxide, or metal salt catalysts.<br />
Cuprous oxide at a prepreg surface layer attracts more cyanate ester<br />
resins but less bismaleimide resin from the prepreg to its surface than the<br />
cupric oxide. A copper surface affects the curing extent of the BT resin in<br />
contact <strong>and</strong> the cupric oxide has a more pronounced effect than the cuprous<br />
oxide. This surface effect can extend at least two microns deep into the BT<br />
prepreg from the contacted interface. 43 The thermal degradation of BT<br />
resins results mainly from the epoxy constituent. However, in the presence<br />
of copper oxides, the degradation in the BT occurs not only in the epoxy<br />
resin but also in the cyanate ester component.<br />
The incorporation of cyanate ester into an epoxy resin improves the<br />
flexural <strong>and</strong> impact strength. The incorporation of bismaleimide (BMI)<br />
increases the stress strain properties with a reduction in impact strength.<br />
The moisture resistance increases with both increasing cyanate ester <strong>and</strong><br />
BMI content.<br />
44, 45<br />
However, glass transition temperature <strong>and</strong> heat deflection temperature<br />
decrease with increasing cyanate ester content. The incorporation of
388 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
bismaleimide into an epoxy resin enhances the thermal properties according<br />
to its percentage of content. 46<br />
The addition of bismaleimide to a cyanate ester results in an increase<br />
in fracture toughness. Dynamic mechanical analysis suggests two glass<br />
transition temperatures. This indicates that the material has a two-phase<br />
morphology <strong>and</strong> can be addressed as an interpenetrating network. 47<br />
For interpenetrating polymer networks based on BMI resin <strong>and</strong> cyanate<br />
ester resins, a BMI resin modified with 2,2 ′ -diallyl bisphenol A was<br />
utilized. Thermal curing with a cyanate ester resin results in an interpenetrating<br />
network.<br />
The flexural strength, flexural strain at break, <strong>and</strong> impact strength<br />
of such a cured resin is lower than that calculated by a linear contribution.<br />
Single damping peaks are detected for the cured resin systems, which<br />
suggests a substantial degree of interpenetration between two networks. 28<br />
At the gel point, the storage modulus G ′ <strong>and</strong> loss modulus G ′′ of the IPN<br />
follow a power law with the oscillation frequency. 48 BMI/ DBA-CE IPN<br />
resin systems combine a low dielectric constant <strong>and</strong> loss, high-temperature<br />
resistance, <strong>and</strong> good processability. 49<br />
2,2-bis(4-cyanatophenyl)propane, <strong>and</strong> a 2,2-bis[4-(4-maleimido<br />
phenoxy)phenyl]propane, have a similar backbone structure. The monomer<br />
blend shows a eutectic point at equimolar composition with a melting<br />
point of 15°C. When cured together in a bismaleimide-triazine network,<br />
polymers of varying compositions can be obtained. The simultaneous curing<br />
of the blend can be transformed to a sequential curing by catalyzing<br />
the dicyanate curing process using dibutyltin dilaurate. The cured blends<br />
undergo a two-stage decomposition, corresponding to the poly(cyanurate)<br />
<strong>and</strong> poly(bismaleimide). 50<br />
10.7.4 Siloxane Crosslinked Resins<br />
Cyanate ester monomers linked to dimethylsiloxane are cured in the same<br />
way as cyanate esters by a cyclotrimerization of the cyanate group to a<br />
cyanurate structure.<br />
The cured resins are homogeneous rubbery castings with T g ranging<br />
from 15 to −43°C. The dielectric constants show a strong dependence on<br />
frequency. The tanδ increases with the chain length of the siloxane but<br />
exhibits only a small frequency dependence. 51
Cyanate Ester Resins 389<br />
Table 10.3: Thermoplastic Modifiers for Cyanate Ester Resins<br />
Thermoplastic Modifier<br />
Reference<br />
Poly(ether imide)<br />
52<br />
Maleimide-styrene terpolymers<br />
53<br />
Polyarylates<br />
54<br />
Polysulfones<br />
55<br />
Polyoxypropylene glycol<br />
56<br />
10.7.5 Alloys with Thermoplastics<br />
Cyanate esters can be alloyed with thermoplastics. This improves the fracture<br />
toughness <strong>and</strong> the moisture resistance. Thermoplastic modifiers are<br />
summarized in Table 10.3<br />
10.7.5.1 Poly(ether imide)<br />
Bisphenol A dicyanate blends with a poly(ether imide) exhibit a phase separation<br />
during curing. The poly(ether imide) phase separates at the early<br />
stages of curing, before gelation, but this phase separation does not affect<br />
the kinetics of the cyclotrimerization. 57<br />
The phase structure changes from a separated phase, via a co-continuous<br />
phase, to phase inversion with the increase of the content of poly(ether<br />
imide). The co-continuous phase morphology is attributed to a spinodal<br />
decomposition. The admixture of poly(ether imide) increases the tensile<br />
strength <strong>and</strong> elongation at break. Time resolved light scattering indicates<br />
that the evolution of the phase separation is governed by a viscoelastic relaxation<br />
process.<br />
52, 58<br />
10.7.5.2 Maleimide-Styrene Terpolymers<br />
A terpolymer composed of N-Phenylmaleimide, N-(p-hydroxy)phenylmaleimide<br />
<strong>and</strong> styrene has pendent reactive p-hydroxyphenyl groups. This<br />
polymer was used to improve the toughness of cyanate ester resins. Copolymers<br />
composed of N-phenylmaleimide <strong>and</strong> styrene are also effective.<br />
An increase in the fracture toughness up to 135% could be achieved, with<br />
a slight loss of flexural strength but retention of flexural modulus <strong>and</strong> glass<br />
transition temperature. 53
390 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
The styrene-hydroxyphenyl maleimide copolymer does not impair<br />
the mechanical properties of cyanate ester resins, in contrast to other modifiers.<br />
22<br />
10.7.5.3 Polyarylates<br />
Polyarylates prepared from bisphenol A <strong>and</strong> phthaloyl chloride <strong>and</strong> the<br />
diacid dichlorides are soluble in a cyanate ester resin <strong>and</strong> can be used to<br />
improve the brittleness of the resin.<br />
The polyarylates include poly(2,2-di(4-phenylene)propane phthalate)<br />
(PPA), poly(2,2-di(4-phenylene)propane phthalate-co-2,2-di(4-phenylene)propane<br />
isophthalate) (IPPA), <strong>and</strong> poly(2,2-di(4-phenylene)propane<br />
phthalate-co-2,2-di(4-phenylene)propane terephthalate) (TPPA). The most<br />
effective modification of the cyanate ester resin can be attained under the<br />
condition of a co-continuous phase structure of the modified resin.<br />
54, 59<br />
10.7.5.4 Polysulfones<br />
The miscibility of bisphenol A dicyanate <strong>and</strong> polysulfone decreases with<br />
an increase in molecular weight of the polysulfone. Concomitantly, the<br />
viscosity of the blend increases. During curing, the phase separation mechanism<br />
depends on the viscosity of the blends. At the onset point of phase<br />
separation, the viscosity determines the morphology of the blends.<br />
Increasing viscosity suppresses the nucleation <strong>and</strong> growth. Therefore,<br />
the viscosity of the blends at the onset point of phase separation is the<br />
critical parameter that determines the morphology of the blends. 55<br />
10.7.5.5 <strong>Reactive</strong> Blending<br />
Inhomogeneous modified poly(cyanurate)s have been created by reactive<br />
blending of a bisphenol A dicyanate ester <strong>and</strong> polyoxypropylene glycol<br />
(PPG). A finely divided morphology with highly interpenetrated phases,<br />
i.e., a poly(cyanurate) rich phase, a mixed phase, <strong>and</strong> a polyoxypropylene<br />
glycol rich phase is formed.<br />
The glass transition temperature of the modified network matrix at<br />
increasing PPG content is lowered. This is attributed due to the incorporation<br />
of PPG in the network, the decrease of the final conversion of the<br />
cyanate, <strong>and</strong> the increase of the free polyoxypropylene glycol which acts<br />
as plasticizer. 56
Cyanate Ester Resins 391<br />
10.7.6 Coupling Agents for Cyanate Ester Resins<br />
Cyanate ester resins have utility in a variety of composite, adhesive, <strong>and</strong><br />
coating applications, where adhesion between the cyanate ester resin <strong>and</strong> a<br />
surface is of critical importance. A coupling agent to enhance the adhesion<br />
is 3-glycidoxypropyltrimethoxysilane.<br />
3-(2-cyanatophenyl)propyltrimethoxysilane or 3-(4-cyanatophenyl)-<br />
propyltrimethoxysilane can be synthesized from 2-allylphenol or 4-allylphenol,<br />
respectively <strong>and</strong> trimethoxysilane. A Karstedt catalyst is used for<br />
the hydrosylilation. 60<br />
The cyanate ester formulations including the coupling agent can be<br />
coated or mixed with a substrate to provide coated composites or filled<br />
molded articles.<br />
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11<br />
Bismaleimide Resins<br />
Bismaleimide resin systems are noted for their high-strength, high-temperature<br />
performance, particularly as matrix resins in fiber-reinforced prepregs<br />
<strong>and</strong> composites. They are bridging the gap between the relatively low temperature-resistant<br />
epoxy systems <strong>and</strong> the very high temperature-resistant<br />
polyimides. Unfortunately, bismaleimides are somewhat brittle, <strong>and</strong> thus<br />
subject to impact induced damage.<br />
11.1 MONOMERS<br />
Monomers for bismaleimide resins are summarized in Table 11.1 <strong>and</strong> are<br />
shown in Figure 11.1.<br />
11.1.1 4,4 ′ -Bis(maleimido)diphenylmethane<br />
The most important monomer is 4,4 ′ -bis(maleimido)diphenylmethane<br />
(BMI). BMI has a melting temperature of 155 to 156°C <strong>and</strong> it polymerizes<br />
radically above the melting point. Networks resulting from BMI are very<br />
brittle.<br />
11.1.2 2,2 ′ -Diallyl bisphenol A<br />
BMI can be used together with 2,2 ′ -Diallyl bisphenol A (DBA). DBA copolymerizes<br />
with BMI. The reaction is an ene reaction that leads to a chain<br />
397
398 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Compound<br />
Table 11.1: Monomers for Bismaleimide Resins<br />
4,4 ′ -Bis(maleimido)diphenylmethane (BMIM) a<br />
Bisphenol A bismaleimide (BMIP) b<br />
2,2-Bis[4-(4-maleimido phenoxy)phenyl]propane (BMIP) b<br />
2,2 ′ -Diallyl bisphenol A (DBA)<br />
1,3-Bis(maleimidomethyl)cyclohexane<br />
1<br />
Multi Ring Maleimides<br />
2<br />
N,N-4,4-Diphenylmethanebismaleimide<br />
3<br />
N,N-4,4-Diphenyl ether bismaleimide (BMIE)<br />
3<br />
N,N-4,4-dibenzylbismaleimide<br />
3<br />
Bis(4-maleimidophenyl)sulfone (BMIS)<br />
1,6-Hexane bismaleimide<br />
4<br />
Divalent metal bismaleimides<br />
5<br />
4-(N-maleimidophenyl)glycidyl ether (MPGE)<br />
6<br />
4,4 ′ -Bismaleimidophenylphosphonate<br />
7<br />
Reference<br />
Bismaleimide bisimides<br />
8<br />
Imides with pendant naphthalene<br />
9<br />
Ester-containing bismaleimides<br />
10, 11<br />
Cardo ester bismaleimides<br />
12<br />
Poly(aminoaspartimide)s<br />
12<br />
a also BMI, BMDPM <strong>and</strong> BDM, however BMI is used in general<br />
for bismaleimides<br />
b BMIP is not uniquely used in the literature. BMIP st<strong>and</strong>s for<br />
either Bisphenol A bismaleimide or 2,2-Bis[4-(4-maleimido<br />
phenoxy)phenyl]propane
Bismaleimide Resins 399<br />
O<br />
O<br />
N<br />
CH 2<br />
N<br />
O<br />
O<br />
BMIM<br />
O<br />
O<br />
N<br />
O<br />
N<br />
O<br />
O<br />
BMIE<br />
O<br />
O<br />
O<br />
N<br />
S<br />
N<br />
O<br />
O<br />
O<br />
BMIS<br />
O<br />
O<br />
CH 3<br />
N<br />
O<br />
C<br />
O<br />
N<br />
O<br />
CH 3<br />
BMIP<br />
O<br />
O<br />
O<br />
N<br />
O<br />
S<br />
O<br />
O - M2+ - O<br />
O<br />
S<br />
O<br />
Divalent metal bismaleimide<br />
N<br />
O<br />
O<br />
Figure 11.1: Bis(4-maleimidophenyl)methane (BMIM), Bis(4-maleimidophenyl)ether<br />
(BMIE), Bis(4-maleimidophenyl)sulfone (BMIS), 2,2-Bis[4-(4-maleimido<br />
phenoxy)phenyl]propane (BMIP), Divalent metal bismaleimide
400 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
extension reaction. Subsequently a Diels-Alder reaction follows. Such copolymers<br />
exhibit less brittleness, because the crosslinking density is less<br />
than that of pure BMI resins. Mixtures of 2,2 ′ -Diallyl bisphenol A ether<br />
<strong>and</strong> 1,4-diallyl phenyl ether also have been used. These compounds are<br />
reactive diluents for BMI because they reduce the apparent viscosity of the<br />
BMI. 13 N,N ′ -Diallyl p-phenyl diamine (DPD) is a reactive diluent in this<br />
sense. Reducing the viscosity is important for the preparation of the advanced<br />
composites by techniques such as resin transfer molding (RTM). 14<br />
For example, instead using diallyl bisphenol A, a novolak resin can<br />
be obtained from diallyl bisphenol A <strong>and</strong> formaldehyde using p-toluenesulfonic<br />
acid as catalyst. The resin is then reactively blended with bisphenol<br />
A bismaleimide (BMIP) <strong>and</strong> cured through an Alder-ene reaction<br />
at high temperatures. The materials are useful as adhesives. 15 The lap<br />
shear strength properties are not significantly affected by the structure of<br />
the particular BMI used. It has been demonstrated that using 2,2 ′ -Diallyl<br />
bisphenol A gives products with better adhesion at elevated temperature. 16<br />
11.1.3 Poly(ethylene glycol) End-capped with Maleimide<br />
The addition of maleimido end-capped poly(ethylene glycol) (PEG) to<br />
a bismaleimide resin (4,4 ′ -bis(maleimido)diphenylmethane) (BDM) enhances<br />
the processability of the BDM resin significantly. The processing<br />
temperatures of the BDM resin increase from approximately 20 to 80°C.<br />
However, the modified resins show a decreased thermal stability of the<br />
blended BDM resin, <strong>and</strong> the coefficient of thermal expansion increases.<br />
The curing behavior <strong>and</strong> the thermal <strong>and</strong> mechanical properties are independent<br />
of the molecular weight of the PEG segment. 17<br />
11.1.4 Bismaleimide Bisimides<br />
The monomers for bisimide resins are prepared by reacting N,N ′ -(4-aminophenyl)-p-benzoquinone<br />
diimine (QA) with maleic anhydride or 5-norbornene-2,3-dicarboxylic<br />
anhydride (also called nadic anhydride) in glacial<br />
acetic acid as shown in Figure 11.2. The cured resins exhibit a char residue<br />
at 800°C in nitrogen atmosphere greater than 55%. Chain-extended types<br />
with flexible ether linkages, i.e., 1,3-bis(4-maleimido phenoxy)benzene or<br />
1,4-bis(4-maleimido phenoxy)benzene, show a lower thermal stability than<br />
the neat resins. 8
Bismaleimide Resins 401<br />
O<br />
O<br />
N<br />
N<br />
N<br />
N<br />
O<br />
O<br />
O<br />
O<br />
O<br />
H 2 N<br />
N N<br />
NH 2<br />
O<br />
O<br />
O<br />
O<br />
O<br />
N<br />
N<br />
N<br />
N<br />
O<br />
O<br />
Figure 11.2: Bismaleimide Adducts of N,N ′ -(4-Aminophenyl)-p-benzoquinone<br />
diimine with Maleic anhydride <strong>and</strong> Nadic anhydride 8
402 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
11.1.5 Maleimide Epoxy Monomers<br />
The use of 4-(N-maleimidophenyl)glycidyl ether (MPGE) is a convenient<br />
approach for synthesizing BMIs with epoxy linkage backbones. 6 MPGE is<br />
synthesized from N-(4-hydroxyphenyl)maleimide <strong>and</strong> epichlorohydrin by<br />
using benzyltrimethylammonium chloride as a catalyst. 18<br />
In a similar manner, maleimide-modified epoxy compounds can be<br />
prepared from N-(4-hydroxyphenyl)maleimide (HPM) with the diglycidyl<br />
ether of bisphenol A. 19 The reaction scheme is shown in Figure 11.3. Triphenylphosphine<br />
<strong>and</strong> methylethylketone were utilized as catalyst <strong>and</strong> solvent,<br />
respectively. The resulting compounds bear both the oxirane ring <strong>and</strong><br />
the maleimide group.<br />
Curing can be achieved by amine curing agents, such as 4,4 ′ -diaminodiphenylmethane<br />
(DDM) <strong>and</strong> dicy<strong>and</strong>iamide (DICY). The incorporation<br />
of maleimide groups into epoxy resins provides a cyclic imide structure<br />
<strong>and</strong> high crosslinking density. The cured resins show high char yields<br />
<strong>and</strong> high LOI values up to 30.<br />
Further, specific chemical groups can be introduced into the BMI<br />
bridging linkages, such as silicon groups <strong>and</strong> phosphorus groups. The dimerization<br />
is shown in Figure 11.4. The cured resin with silicone exhibits<br />
a limiting oxygen index of greater than 50.<br />
11.1.6 Phosphorous-containing Monomers<br />
A phosphorus-containing bismaleimide (BMI) monomer, bis(3-maleimidophenyl)phenylphosphine<br />
oxide (BMIPO), can be accessed by the<br />
imidization of bis(3-aminophenyl)phenylphosphine oxide. This bismaleimide<br />
exhibits a good solubility in common organic solvents <strong>and</strong> a wide<br />
processing window. 20, 21 It is an excellent flame retardant with a high glass<br />
transition temperature, high onset decomposition temperature, <strong>and</strong> high<br />
limiting oxygen index. Copolymers with BMIPO, BMI, <strong>and</strong> epoxy based<br />
4,4 ′ -methylenedianiline (DDM) are homogeneous products without phase<br />
separation. 22<br />
Epoxy resins can be modified by 3,3 ′ -bis(maleimidophenyl)phenylphosphine<br />
oxide. The cured resins have good thermal properties. 23 Further,<br />
phenyl-(4,4 ′ -bismaleimidophenyl)phosphonate <strong>and</strong> ethyl-(4,4 ′ -bismaleimidophenyl)phosphonate<br />
were tested as flame retardants in epoxy<br />
systems. The flame retardancy of phosphonate-containing epoxy systems<br />
was improved significantly with BMI. 24 An increase of the BMI com-
Bismaleimide Resins 403<br />
O<br />
O<br />
O + H 2 N<br />
OH<br />
N<br />
OH<br />
O<br />
O<br />
O<br />
CH 2<br />
CH<br />
O<br />
CH 2<br />
CH<br />
CH 2<br />
CH 2<br />
O<br />
O<br />
H 3 C<br />
C CH 3<br />
H 3 C<br />
C CH 3<br />
O<br />
N<br />
O<br />
O<br />
+<br />
O<br />
CH 2<br />
O<br />
CH 2<br />
O<br />
CH<br />
CH 2<br />
OH<br />
N<br />
O<br />
CH OH<br />
CH 2<br />
O<br />
Figure 11.3: Synthesis of Epoxy-modified Maleimide Monomers 19
404 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
N<br />
O<br />
O CH 2 CH CH 2<br />
O<br />
MPGE<br />
HO<br />
R<br />
OH<br />
O<br />
OH<br />
N<br />
O CH 2 CH<br />
O<br />
CH 2<br />
O<br />
R<br />
O<br />
O<br />
CH 2<br />
CH CH 2 O<br />
N<br />
OH<br />
O<br />
R= one of the following groups<br />
CH 3<br />
C<br />
CH 3<br />
O P O<br />
Si<br />
Figure 11.4: Dimerization of 4-(N-maleimidophenyl)glycidyl ether (MPGE) with<br />
Functional Diols
Reaction Type<br />
Table 11.2: Reactions of Maleimides<br />
Bismaleimide Resins 405<br />
Radical polymerization<br />
Diels-Alder reaction with a pentamathylcyclopentadiene<br />
derivative<br />
25<br />
Diels-Alder reaction with furans<br />
26<br />
Reference<br />
pounds also increased the storage modulus <strong>and</strong> glass transition temperature<br />
but reduced the mechanical strength of the epoxy blends.<br />
More bulky phosphorous-containing bismaleimides have been obtained<br />
by the reaction of 9,10-dihydro-9-oxa-10-phosphaphenanthrene-<br />
10-oxide (DOPO) <strong>and</strong> 4,4 ′ -bis(maleimido)diphenylmethane.<br />
27, 28<br />
The<br />
glass transition temperatures of the cured resins decrease with phosphorus<br />
content. The limiting oxygen index (LOI) is improved by the incorporation<br />
of DOPO.<br />
11.1.7 Multiring Monomers with Pendant Chains<br />
The synthesis of multiring monomers with long pendant chains is shown<br />
in Figure 11.5. The synthesis runs via a two-fold Friedel-Crafts reaction,<br />
followed by a reduction of the dinitro compounds. The diamines are then<br />
reacted with maleic anhydride into bismaleimides. The properties of the<br />
crosslinked poly(benzylimide) are not strongly affected by the presence<br />
of the long alkyl chains. Therefore, linear thermoplastic polyimides with<br />
good thermal stability can be obtained. 2<br />
11.1.8 Reactions of Maleimides<br />
We summarize some of the reactions of maleimides, all of them suitable<br />
for obtaining polymers. The reactions are given in Table 11.2.<br />
11.1.8.1 Radical Polymerization<br />
The double bond in the maleic group undergoes an ordinary radical polymerization.
406 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
CH 3<br />
+ Cl CH<br />
H CH 2<br />
NO 2<br />
3 C<br />
3<br />
R<br />
R=C 16 H 33 ;C 8 H 17 ;C 6 H 13<br />
O 2 N<br />
CH 3<br />
H 2 C CH 2<br />
NO 2<br />
H 3 C<br />
R<br />
CH 3<br />
H 2 N<br />
CH 3<br />
H 2 C CH 2<br />
NH 2<br />
H 3 C<br />
R<br />
CH 3<br />
O<br />
O<br />
O<br />
O<br />
O<br />
CH 3<br />
N<br />
H 2 C<br />
CH 2<br />
N<br />
O<br />
H 3 C<br />
R<br />
CH 3<br />
O<br />
Figure 11.5: Multiring Monomers with Flexible Side Chains 2
Bismaleimide Resins 407<br />
11.1.8.2 Michael Addition<br />
The Michael addition is an addition of resonance-stabilized carbanions to<br />
activated double bonds. The Michael addition is thermodynamically controlled.<br />
It was first described in 1887. 29<br />
α,ω-Polyaminoglycols. Amino-terminated oligomers based on propylene<br />
glycol, ethylene glycol, <strong>and</strong> dimethylsiloxane, have been chain-extended<br />
via Michael additions with bismaleimides. The polymers have a degree<br />
of polymerization up to 15. The polymers are either linear or crosslinked,<br />
depending on the starting materials <strong>and</strong> the conditions of preparation.<br />
30, 31<br />
Maleimide-urethanes. The reaction of 4-maleimidophenyl isocyanate<br />
<strong>and</strong> oligoether diols or oligoester diols results in bismaleimide-containing<br />
urethane groups. The bismaleimides can be chain-extended by means of a<br />
Michael reaction into linear polymers. 32 The reaction scheme is shown<br />
in Figure 11.6. Chain extenders are 4,4 ′ -diaminodiphenylmethane <strong>and</strong><br />
4,4 ′ -oxydianiline. Elastic films are obtained that show good mechanical<br />
properties <strong>and</strong> a better thermal stability than the traditional polyurethane<br />
elastomers.<br />
11.1.8.3 Diels-Alder Reaction<br />
Chain Extension. Bismaleimide oligomers can be synthesized by chain<br />
extension reaction utilizing a Diels-Alder reaction as shown in Figure 11.7.<br />
In the first step, a bisfuranylmethylcarbamate is formed from toluene diisocyanate<br />
(TDI), or hexamethylene diisocyanate with two mol of furfuryl<br />
alcohol. The furan (via its double bonds) then reacts with a bismaleimide,<br />
such as 4,4 ′ -bis(maleimido)diphenylmethane using a Diels-<br />
Alder reaction. 33 These bismaleimide oligomers can be used as a toughness<br />
modification agent for other BMI resins. Finally, the ether link in the<br />
original furan moiety is eliminated by acetic anhydride, <strong>and</strong> replaced by an<br />
aromatic group.<br />
Furan-containing Adducts. Furan-terminated compounds react with<br />
BMI at 70°C to an oxygen-containing cycloadduct. The simple adducts are<br />
obtained from the monofunctional dienophiles. Crosslinked products are<br />
obtained from the coupling of furanic polymers with the bisdienophiles. 26
408 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
O<br />
N<br />
NCO + HO OH + OCN<br />
N<br />
O<br />
O<br />
O<br />
O<br />
C<br />
O<br />
O<br />
O<br />
C<br />
O<br />
N<br />
NH<br />
HN<br />
N<br />
O<br />
O<br />
H 2 N<br />
O NH 2<br />
4,4’-Oxydianiline<br />
H 2 N<br />
CH 2 NH 2<br />
4,4’-Diaminodiphenylmethane<br />
Figure 11.6: Dimaleimide urethanes <strong>and</strong> Michael Reaction with aromatic Diamines
Bismaleimide Resins 409<br />
O<br />
CH 2 OH OCN R<br />
NCO+<br />
HO<br />
CH 2<br />
O<br />
O<br />
O<br />
O<br />
CH 2<br />
O C<br />
HN<br />
R<br />
C O<br />
NH<br />
CH 2<br />
O<br />
O<br />
N<br />
O<br />
O O<br />
CH 2 O C C O<br />
O<br />
HN R NH<br />
CH 2<br />
O<br />
O O<br />
O O<br />
N<br />
N<br />
O<br />
O<br />
CH 3<br />
C<br />
O<br />
C<br />
CH 3<br />
O<br />
O<br />
CH 2<br />
O<br />
C<br />
C<br />
O<br />
CH 2<br />
O<br />
N<br />
O<br />
HN<br />
R<br />
NH<br />
O<br />
N<br />
O<br />
Figure 11.7: Chain Extension Reaction
410 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
On heating the polymerized materials in various solvents with high boiling<br />
points, no soluble products were obtained. This indicates the absence of a<br />
retro Diels-Alder reaction.<br />
It was concluded that aromatization of the imino heterocycles arising<br />
from the cycloaddition took place, resulting in irreversible crosslinks. For<br />
example, 1,1 ′ -(1-methylethylidene)bis(4-(1-(2-furanylmethoxy)-2-propanolyloxy))benzene<br />
reacts with several bismaleimides, such as N,N ′ -hexamethylenebismaleimide<br />
<strong>and</strong> N,N ′ -p-phenylenedimaleimide. In a subsequent<br />
polymerization in the presence of acetic anhydride the aromatization<br />
of the tetrahydrophthalimide intermediates occurs. 34<br />
Networks from the linear copolymer Poly(styrene-co-furfuryl methacrylate)<br />
can be prepared by Diels-Alder reaction at 25°C by adding bismaleimide.<br />
35 In such a crosslinked copolymer, an endothermic peak without<br />
a glass transition is observed. On reheating the sample, a glass transition<br />
is found. This is attributed to the formation of a linear copolymer<br />
produced by the retro Diels-Alder reaction in the course of the first heat<br />
treatment. 36<br />
Bisdienes. Phenylated poly(dihydrophthalimide)s have been synthesized<br />
from 3,3 ′ -(oxydi-p-phenylene)bis(2,4,5-triphenylcyclopentadienone),<br />
3,3 ′ -(p-phenylene)bis(2,4,5-triphenylcyclopentadienone), N,N ′ -o-phenylenedimaleimide,<br />
N,N ′ -m-phenylenedimaleimide, <strong>and</strong> N,N ′ -p-phenylenedimaleimide.<br />
37 Ketonic adducts are formed as intermediates, but the carbon<br />
monoxide evolution proceeds spontaneously. Difunctional cyclohexadienes<br />
with dihydrophthalimide as central units can act as bisdienes in Diels-Alder<br />
polymerization polyadditions with bis(4-(1,2,4-triazoline-3,5-dione-4-yl)phenyl)methane<br />
as the difunctional dienophile. The introduction<br />
of phenyl side groups increases the solubility. 38<br />
Pyrones. Pyrones also behave as diene <strong>and</strong> react with bismaleimides,<br />
thus forming a bis-cycloadduct. 39<br />
Diabietylketone. Another bisdiene is the dehydrodecarboxylation product<br />
of abietic acid, also addressed as diabietylketone. 40 The dehydrodecarboxylation<br />
reaction is shown in Figure 11.8. A Diels-Alder polymerization<br />
of diabietylketone with 4,4 ′ -diphenylmethanedimaleimide (bismaleimide)<br />
is possible. The resulting polymer is expected to be a poly-<br />
(ketoimide) with hydrophenanthrene moieties in the backbone. However,
Bismaleimide Resins 411<br />
C<br />
O<br />
COOH<br />
Figure 11.8: Dimerization of Abietic Acid by Dehydrodecarboxylation<br />
it was found that the repeating units are bismaleimide <strong>and</strong> diabietylketone<br />
units not in a molar ratio of 1:1, but in a ratio of 5:1 to 6:1. This<br />
observation was explained by the difference between the rates of the two<br />
concomitant reactions, i.e., the homopolymerization of bismaleimide <strong>and</strong><br />
the Diels-Alder polymerization.<br />
On the other h<strong>and</strong>, a polymer of the two monomer units in a ratio<br />
of 1:1 can be obtained by the dehydrodecarboxylation of the diacid resulting<br />
from the Diels-Alder reaction between abietic acid <strong>and</strong> 4,4 ′ -diphenylmethanedimaleimide<br />
<strong>and</strong> also by the polycondensation of the ketone of<br />
maleated abietic acid with 4,4 ′ -diaminodiphenylmethane. The polymers<br />
are stable in air up to 360°C.<br />
Photochemical Generation of Dienes. Certain dienes, such as o-quinodimethanes<br />
can be generated by photochemical reactions. 41 When the photochemical<br />
generation occurs in the presence of bismaleimides, the dienes<br />
may react immediately with the bismaleimide in a Diels-Alder reaction,<br />
thus forming a polymer.<br />
Naphthols. Several 2-naphthols undergo a Diels-Alder addition reaction<br />
with maleimides. This reaction can be utilized in curing bismaleimides.<br />
For example, 7-allyloxy-2-naphthol satisfactorily cures bismaleimides. 42
412 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Urethane-imides. Poly(ester-urethane-imides) can be prepared by the<br />
Diels-Alder polyaddition of 1,6-hexamethylene-bis(2-furanylmethylcarbamate)<br />
with various bismaleimides that contain ester groups in the backbone.<br />
43<br />
Triol Extenders. Poly(bismaleimide-ether) polymers with functional<br />
pendant groups can be obtained from a Michael polyaddition of flexible<br />
bismaleimides, such as N,N-4,4-diphenylmethanebismaleimide, N,N-<br />
4,4-diphenyl ether bismaleimide <strong>and</strong> N,N-4,4-dibenzylbismaleimide to trifunctional<br />
monomers, such as glycerol <strong>and</strong> phenolphthalein. Additionally,<br />
the hydroxyl functional poly(bismaleimide-ether) can be modified with<br />
cinnamoyl moieties. 3<br />
Hyperbranched Polyamides. Monomers that contain the diphenylquinoxaline<br />
group are 2,3-bis(4-aminophenyl)quinoxaline-6-carboxylic acid<br />
(BAQ) <strong>and</strong> 2,3-bis(4-(4-aminophenoxy)phenyl)quinoxaline-6-carboxylic<br />
acid (BAPQ), c.f. Figure 11.9.These compounds form hyperbranched aromatic<br />
polyamides on polycondensation.<br />
Although the monomers are structurally similar, the properties of<br />
both monomers <strong>and</strong> the respective hyperbranched polymers are different.<br />
BAQ reacts normally with BMI in a Michael addition fashion, followed by<br />
homopolymerization of the excess BMI. However, BAPQ seems to initiate<br />
a free radical polymerization of BMI at room temperature. This unexpected<br />
property of BAPQ suggests it can be used as a prototype for the development<br />
of low-temperature, thermally curable thermosetting resin systems<br />
for high-temperature applications. 44<br />
11.1.9 Specialities<br />
11.1.9.1 1,3-Bis(maleimidomethyl)cyclohexane<br />
Imides are often substantially insoluble in ordinary organic solvents <strong>and</strong><br />
are soluble only in high boiling aprotic polar solvents, such as N-methyl-<br />
2-pyrrolidone, N,N-dimethylacetamide, etc. This is a drawback when impregated<br />
varnishes are prepared by dissolving the imides in these solvents.<br />
High temperature is required for removing the solvents <strong>and</strong> the solvents<br />
are liable to remain in the prepregs formed from the varnishes, causing<br />
foaming in the laminates <strong>and</strong> considerably lowering the quality of flexible<br />
printed circuits (FPC).
Bismaleimide Resins 413<br />
COOH<br />
N<br />
NH 2<br />
N<br />
NH 2<br />
2,3-Bis(4-aminophenyl)quinoxaline-6-carboxylic acid<br />
COOH<br />
N<br />
O<br />
NH 2<br />
N<br />
O<br />
NH 2<br />
2,3-Bis[4-(4-aminophenoxy)phenylquinoxaline-6-carboxylic acid<br />
Figure 11.9: Monomers for Hyperbranched Oligoamides 44
414 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
1,3-Bis(maleimidomethyl)cyclohexane is a bismaleimide compound<br />
that is readily soluble in a variety of ordinary low boiling point organic solvents.<br />
1 For instance, it is soluble in acetone, methylethylketone, tetrahydrofuran,<br />
chloroform, <strong>and</strong> N,N-dimethylformamide. Despite its aliphatic<br />
structure, the monomer can provide good heat-resistant bismaleimide resins<br />
by thermal polymerization.<br />
11.1.9.2 Siliconized Bismaleimides<br />
Siliconized epoxy-1,3-bis(maleimido)benzene has been synthesized from<br />
siloxanes.<br />
45, 46<br />
In the first step, epoxy based on the diglycidyl ether of<br />
bisphenol A, <strong>and</strong> 4,4 ′ -diaminodiphenylmethane (DDM) was extended with<br />
(3-aminopropyl)triethoxysilane.<br />
The pendent ethoxysilane groups were further reacted with a hydroxy-terminated<br />
poly(dimethylsiloxane) (HTPDMS) with dibutyltin dilaurate<br />
as catalyst. The scheme is shown in Figure 11.10. 1,3-Bis(maleimido)benzene<br />
is prepared from m-phenylene diamine <strong>and</strong> maleic anhydride.<br />
Finally, the 1,3-bis(maleimido)benzene is dissolved in the siliconized epoxy<br />
system at 125°C. To this mixture, a stoichiometric amount of DDM<br />
is added homogenized. This mixture is cured at 120°C for 1 hour <strong>and</strong><br />
postcured at 205°C.<br />
The curing is a comparatively complex process. It is proposed that<br />
the curing is due to the following reactions: 46<br />
1. Oxirane ring opening reaction with active amine hydrogens,<br />
2. Autocatalytic reaction of the oxirane ring with pendent hydroxyl<br />
groups of epoxy resin,<br />
3. Addition reaction of the amine groups of DDM with double bonds<br />
of BMI (Michael addition), <strong>and</strong><br />
4. Homopolymerization reaction of BMI.<br />
Bismaleimides with silicone linkages can also be prepared via the<br />
Diels-Alder reaction of bismaleimide-containing silicone <strong>and</strong> bisfuran containing<br />
silicone. The bismaleimides are soluble in low boiling point solvents,<br />
<strong>and</strong> the cured resins are stable up to 350 to 385°C. 47<br />
Still another reaction path to prepare bismaleimides with silicone<br />
groups is the reaction of N-(4-hydroxyphenyl)maleimide with dichlorodimethylsilane.<br />
In a second step, the adduct is reacted with a polysiloxane<br />
that is terminated with hydroxyl groups. 48
Bismaleimide Resins 415<br />
CH 2<br />
CH CH 2 + H N H + CH 2 CH 2<br />
O<br />
OCH<br />
CH 2<br />
CH 2<br />
CH 3 CH 2<br />
OH<br />
Si<br />
CH 2<br />
CH 2 CH 3<br />
O Si O<br />
CH 2 OH<br />
+ CH 3<br />
+<br />
+ Si<br />
O<br />
OH<br />
Si<br />
CH 2<br />
CH<br />
OH<br />
N<br />
CH 2<br />
CH 2<br />
CH<br />
OH<br />
CH 2<br />
CH 2<br />
CH 2<br />
Si<br />
O<br />
CH 2<br />
O<br />
Si<br />
O<br />
Si<br />
Si<br />
Figure 11.10: Formation of a Silane-modified Epoxy Resin
416 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
11.1.9.3 Maleimide Phenolic Resins<br />
Phenolic novolak resins with pendant maleimide groups are accessible by<br />
the polymerization of a mixture of phenol <strong>and</strong> N-(4-hydroxyphenyl)maleimide<br />
(HPM) with formaldehyde in the presence of an acid catalyst. 49<br />
HPM is less reactive than phenol toward formaldehyde. In fact, N-phenylmaleimide<br />
is also reactive towards phenol <strong>and</strong> formaldehyde.<br />
Curing is done by both possible typical reaction mechanisms for<br />
these groups. Around 150 to 170°C, there is a condensation reaction of the<br />
methylol groups formed in minor quantities on the phenyl ring of HPM.<br />
The curing at around 275°C is associated with the addition polymerization<br />
reaction of the maleimide groups.<br />
Polymerization studies of non-hydroxy-functional N-phenyl maleimides<br />
indicate that the phenyl groups of these molecules are activated<br />
toward an electrophilic substitution reaction by the protonated methylol<br />
intermediates formed by the acid-catalyzed reaction of phenol <strong>and</strong> formaldehyde.<br />
Allyl-functional Novolak. The maleimide-functional phenolic resin can<br />
be reactively blended with an allyl-functional novolak. This system undergoes<br />
a multistep curing process over a temperature range of 110 to 270°C.<br />
The presence of maleimide reduces the isothermal gel time of the blend.<br />
Increasing the allylphenol content decreases the crosslinking in the<br />
cured matrix, leading to an enhanced toughness <strong>and</strong> to improved mechanical<br />
properties of the resultant composites. Increasing the maleimide content<br />
results in an enhanced thermal stability. 50<br />
Epoxy-functional Novolak. Epoxy-novolak (EPN) resins have been<br />
cured together with a 1,1 ′ -(methylene di-4,1-phenylene)bismaleimide. A<br />
suitably blended EPN <strong>and</strong> BMI with 30% bismaleimide shows higher T g<br />
than the neat resin.<br />
With an increase of bismaleimide, the thermal stability is increased.<br />
A single exothermic reaction is observed on curing. The morphology of<br />
the cured samples indicates the formation of a homogeneous network in<br />
the blends.<br />
51, 52
Compound<br />
Table 11.3: Modifiers<br />
Bismaleimide Resins 417<br />
Reference<br />
2,2 ′ -Diallyl bisphenol A (DBA)<br />
<strong>Reactive</strong> rubbers<br />
Polysulfone<br />
Polyetherimide<br />
53<br />
Poly(hydantoin)<br />
4,4 ′ -Bis(o-propenylphenoxy)benzophenone<br />
N-Phenylmaleimide-styrene copolymer<br />
Acetylene-terminated polymers<br />
2,4-Di(2-allylphenoxy)-6-(2-naphthyloxy)-1,3,5-triazine (DAPNPT)<br />
54<br />
2,4-Di(2-allylphenoxy)-6-N,N-dimethylamino-1,3,5-triazine<br />
55<br />
2,6-Di(4-aminophenoxy)benzonitrile (DAPB)<br />
56<br />
Poly(propylene phthalate)<br />
57<br />
11.2 SPECIAL ADDITIVES<br />
11.2.1 Tougheners <strong>and</strong> Modifiers<br />
The toughness of bismaleimide resins is a major problem that is limiting<br />
the field of application. The toughness can be improved by adding reactive<br />
components that reduce the crosslinking density. Modifiers are summarized<br />
in Table 11.3.<br />
11.2.1.1 <strong>Reactive</strong> Rubbers<br />
Blending with reactive liquid rubbers such as carboxyl-terminated butadiene<br />
acrylonitrile rubbers increases the toughness.<br />
11.2.1.2 Polyetherimide<br />
Polyetherimide (PEI) is highly effective as a toughness improver for a bismaleimide<br />
resin. Increasing the modifier content increases the miscibility<br />
of the two phases. At a content of 20% PEI, the morphological structure<br />
of the modified resin changes from a dispersed system to a particle cocontinuous<br />
structure <strong>and</strong> eventually with still more PEI to a phase inverted<br />
system. 53 Polyetherimide is also used in bismaleimide resins composed of<br />
4,4 ′ -bis(maleimido)diphenylmethane <strong>and</strong> 2,2 ′ -Diallyl bisphenol A.<br />
58, 59
418 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
11.2.1.3 Polyesterimide<br />
Polyesterimides can be used to improve the toughness of bismaleimide<br />
resins, composed of 4,4 ′ -bis(maleimido)diphenylmethane (BDM) <strong>and</strong><br />
2,2 ′ -Diallyl bisphenol A (DBA). The fracture energy of the cured samples<br />
increases with the increase of polyesterimide content in the modified<br />
bismaleimide system. 60<br />
11.2.1.4 Polysiloxanes<br />
The addition of alkenylphenols such as 2-allylphenol, 2-propenylphenol,<br />
<strong>and</strong> 2,2 ′ -diallyl bisphenol A increases the toughness of bismaleimide resin<br />
systems, but the degree of toughness obtained is less than that ultimately<br />
desirable. Polysiloxanes that are capped with alkenylphenols are compatible<br />
with bismaleimide resins <strong>and</strong> can be used in appreciable amounts to<br />
toughen such resins. The toughened systems maintain a high degree of<br />
thermal stability.<br />
A 2-allylphenoxy-terminated diphenyldimethylpolysiloxane can be<br />
prepared from an epoxy-terminated siloxane, 2-allylphenol <strong>and</strong> triphenylphosphine<br />
as catalyst. 61<br />
11.2.1.5 Poly(ether ketone ketone)<br />
Poly(ether ether ketones) (PEEK) to improve the brittleness of the bismaleimide<br />
resin include poly(phthaloyl diphenyl ether) (PPDE), poly(phthaloyl<br />
diphenyl ether-co-isophthaloyl diphenyl ether) (PPIDE), <strong>and</strong> phthaloyl diphenyl<br />
ether-co-terephthaloyl diphenyl ether (PPTDE). The bismaleimide<br />
resin is a mixture of 4,4 ′ -bis(maleimido)diphenylmethane <strong>and</strong> 2,2 ′ -Diallyl<br />
bisphenol A. It was shown that PPIDE with 50 mol-% isophthaloyl unit<br />
is more effective as a modifier for the bismaleimide resin than the other<br />
poly(ether ketone ketone)s. The most effective modification for the cured<br />
resins could be achieved with a co-continuous phase or a phase-inverted<br />
structure of the modified resins. 62<br />
Similarly, in a three-component bismaleimide resin composed<br />
of 4,4 ′ -bis(maleimido)diphenylmethane (BDM), 2,2 ′ -diallyl bisphenol A<br />
(DBA), <strong>and</strong> o,o ′ -dimethallyl bisphenol A, PPIDE <strong>and</strong> PPTDE are more<br />
effective as modifiers than PPDE. 63
Bismaleimide Resins 419<br />
11.2.1.6 Triazines<br />
2,4-di(2-allylphenoxy)-6-(2-naphthyloxy)-1,3,5-triazine (DAPNPT) can<br />
be prepared by the reaction of cyanuric chloride with 2-allylphenol followed<br />
by a treatment with 2-naphthol. 54 The procedure is shown in<br />
Figure 11.11.<br />
Copolymers of DAPNPT with 4,4 ′ -bis(maleimido)diphenylmethane<br />
(BMDPM) show improved mechanical properties compared to pure<br />
BMDPM. The copolymer shows up to 10 times higher impact strength <strong>and</strong><br />
3 times higher shear strength. However, the impact strength <strong>and</strong> the shear<br />
strength dramatically decrease when the molar ratio of DAPNPT/BMDPM<br />
in the copolymer exceeds 1:2.<br />
Completely analogous, as shown in Figure 11.11, 2,4-di(2-allylphenoxy)-6-N,N-dimethylamino-1,3,5-triazine<br />
can be prepared by the reaction<br />
of 2-allylphenol with cyanuric chloride <strong>and</strong> then by dimethylamine.<br />
55 This monomer is a modifier for bismaleimide resins. It effectively<br />
improves the mechanical properties of the resin without greatly decreasing<br />
heat resistance of the resin.<br />
11.2.1.7 Others<br />
Polyamide-imide (PAI), poly(phenylene sulfide) cannot be used in BMI<br />
allyl systems. These compounds have poor miscibilities with allyl compounds.<br />
11.2.1.8 Boric Esters<br />
Boron can be incorporated into allylic compounds by esterification of allylphenol<br />
<strong>and</strong> boric acid. Such compounds are suitable as comonomers in the<br />
polymerization of bismaleimide resins. The cured resins show an excellent<br />
thermal stability.<br />
No weight loss was observed when the copolymer was heated up to<br />
465°C in nitrogen atmosphere. The char yields at 800°C in nitrogen are<br />
more than 50%. 64 Allyl boron compounds improve the ablative properties<br />
of bismaleimide resins. 65
420 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Cl<br />
OH<br />
N<br />
N<br />
+ +<br />
HO<br />
Cl<br />
N<br />
Cl<br />
Cl<br />
N<br />
N<br />
O<br />
N<br />
O<br />
HO<br />
O<br />
N<br />
N<br />
O<br />
N<br />
O<br />
Figure 11.11: Preparation of<br />
2,4-Di(2-allylphenoxy)-6-(2-naphthyloxy)-1,3,5-triazine
Bismaleimide Resins 421<br />
11.2.2 Fillers<br />
11.2.2.1 Aluminum nitride Ceramic Powders<br />
To prevent the failure of integrated circuites (IC) during processing <strong>and</strong><br />
operation, materials with a low dielectric constant, <strong>and</strong> a silicon compatible<br />
coefficient of thermal expansion (CTE) ca. 4.0×10 −6 K −1 are needed.<br />
A low dielectric constant reduces the delay time of signal transmission.<br />
Further, a high glass transition temperature <strong>and</strong> a high conductivity is substantial,<br />
especially in high powered ICs.<br />
Silica has a high thermal conductivity, but it has a high dielectric<br />
constant of around 40. Aluminum nitride 66 has a melting point of 2230°C<br />
<strong>and</strong> is highly chemically inert. It is used in refractory materials, also in<br />
conjunction with silica nitride <strong>and</strong> boron nitride. Aluminum nitride (AlN)<br />
ceramic is superior to silica, since it not only has a high thermal conductivity<br />
of up to 320 W/K <strong>and</strong> a compatible CTE with silicon, but it also has<br />
a relatively low dielectric constant (ca. 8.9).<br />
AlN ceramic powders, used as fillers in a modified bismaleimide resin,<br />
change the curing performance. The addition of AlN increases the<br />
activation energy of curing of the BMI. Also, the glass transition temperature<br />
is raised slightly. 67<br />
11.2.2.2 Silsesquioxane Nanofillers<br />
Silsesquioxane nanofillers in a bismaleimide modified novolak resin exhibit<br />
improvements in the glass transition temperature <strong>and</strong> the heat resistance<br />
of the material. The modulus at high temperatures is also improved.<br />
The particle size of the dispersed phase was about 100 nm, <strong>and</strong> particle<br />
aggregates were observed. 68<br />
11.2.3 Titanium dioxide<br />
Ternary hybrids of bismaleimide-polyetherimide-titanium dioxide were<br />
synthesized by sol-gel reaction. A 10% solution of BMI prepolymer in<br />
N-methyl-2-pyrrolidone was mixed with 30 phr of polyetherimide.<br />
Dibutoxybis(acetylacetonato)titanium(IV) was obtained from tetrabutyltitanate<br />
<strong>and</strong> acetylacetone. This compound was added, <strong>and</strong> after stirring<br />
again tetrabutyltitanate <strong>and</strong> acid were added. After drying, the resulting<br />
film was thermally cured. The titanium dioxide particles were<br />
dispersed uniformly in both the PEI-rich phase <strong>and</strong> the BMI-rich phase,
422 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Compound<br />
Table 11.4: Flame Retardant Bismaleimides<br />
Reference<br />
Bis(3-maleimidophenyl)phenylphosphine<br />
oxide (BMIPO)<br />
3,3 ′ -Bis(maleimidophenyl)phenylphosphine oxide<br />
23<br />
Phenyl-(4,4 ′ -bismaleimidophenyl)phosphonate<br />
24<br />
Ethyl-(4,4 ′ -bismaleimidophenyl)phosphonate<br />
24<br />
9,10-Dihydro-9-oxa-10-phosphaphenanthrene-10-oxide<br />
(DOPO)<br />
20–22<br />
27, 28<br />
having a mean diameter of around 50 nm. 69 Increasing titanium dioxide<br />
content improves the mechanical properties. However, the thermal decomposition<br />
temperatures of the hybrids decrease from 374°C of the unfilled<br />
resin to 294°C of a resin with a titanium dioxide content of 20 phr. It is<br />
believed that titanium dioxide exerts a catalytic effect in this aspect.<br />
11.2.4 Reinforcing Materials<br />
11.2.4.1 Silica Coatings<br />
The usual way to reinforce is to add the reinforcing material to polymeric<br />
materials. For medical applications, ceramic coatings have been applied<br />
to a bismaleimide. Non-reinforced BMI specimens are coated with a thin,<br />
protective layer of a dense silicate ceramic material. Testing of the Vickers<br />
hardness on the coated <strong>and</strong> uncoated BMI specimens indicates that the<br />
coatings adhere well to the substrate. 70<br />
11.2.5 Flame Retardants<br />
Bismaleimide resins are flame retardant, because they are comprised of<br />
aromatic groups <strong>and</strong> nitrogen. Therefore, for many applications, flame<br />
retardancy is not a major problem. Phosphorous-containing monomers<br />
have been described as flame retardants. They are used not only for bismaleimides,<br />
but also for epoxy systems. Flame retardants are shown in<br />
Table 11.4.
Bismaleimide Resins 423<br />
11.3 CURING<br />
11.3.1 Monitoring Curing Reactions<br />
11.3.1.1 DSC<br />
Experimental data for a kinetic model of a modified bismaleimide resin<br />
were obtained by isothermal DSC. A curing mechanism involving multiple<br />
reactions was established. The reaction is dominated by different mechanisms<br />
at different stages of curing. At the beginning of curing, an autocatalytic<br />
reaction was observed. 71 A reaction model was set up, <strong>and</strong> the<br />
activation energy <strong>and</strong> the frequency factor were calculated. 72<br />
11.3.1.2 Dielectric Method<br />
A dielectric sensor for the cure monitoring of high temperature composites<br />
has been developed. The on-line cure monitoring of a bismaleimide resin<br />
was performed using a Wheatstone bridge type circuit <strong>and</strong> a high temperature<br />
dielectric sensor. 73<br />
11.3.1.3 Infrared Spectroscopy<br />
An in-situ technique for studying the polymerization kinetics has been developed.<br />
Fourier self-deconvolution of the spectra was used to enhance the<br />
peak separations <strong>and</strong> the calculation of the peak areas needed for quantitative<br />
monitoring of the curing process. During curing of 1,1 ′ -(methylene<br />
di-4,1-phenylene)bismaleimide (MDP-BMI) with 4,4 ′ -diaminodiphenylmethane<br />
(DDM), a substantial difference in the reactivity between primary<br />
<strong>and</strong> secondary amine was observed. 74<br />
11.3.2 Polymerization<br />
11.3.2.1 Gel Point<br />
When a monomer containing two double bonds is incorporated into a radically<br />
growing chain, it is first incorporated with one double bond only. The<br />
polymer chain then will bear pendant double bonds, but initially no crosslinks.<br />
There are special cases where, after incorporation of the first double<br />
bond, the second, now pendant double bond will be consumed by the same<br />
growing radical. This behavior is termed backbiting, or if it occurs more<br />
r<strong>and</strong>omly, intramolecular cyclization.
424 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
The pendant double bonds may react in a further stage of the polymerization<br />
with another growing chain. Accordingly a complete polymer<br />
chain becomes part of another growing chain by the reaction of a single<br />
pendant double bond. The molecular weight of the polymer grows rapidly<br />
until a certain stage of conversion is reached <strong>and</strong> a gel is formed.<br />
The formation of networks during the copolymerization of styrene<br />
with various maleimide compounds was investigated. 75 In particular, p-<br />
maleimidobenzoic anhydride, or mixtures of p-maleimidobenzoic anhydride,<br />
methyl-p-maleimidobenzoate, <strong>and</strong> styrene were studied.<br />
In resin systems containing bismaleimides, during radical polymerization,<br />
the concentrations of pendent double bonds in copolymers, calculated<br />
from the consumption of monomers <strong>and</strong> copolymer composition,<br />
follow the general trend typical for vinyl-divinyl copolymerization.<br />
At the end of polymerization, a substantial fraction of pendent maleimide<br />
bonds remains in the system. The conversions at the gel point are<br />
much higher than for ring-free copolymerization due to cyclization <strong>and</strong> the<br />
steric hindrance of the pendent double bonds.<br />
11.3.2.2 Thermal Polymerization<br />
In stoichiometric formulations of 1,1 ′ -(methylene di-4,1-phenylene)bismaleimide,<br />
modified with 2,2 ′ -Diallyl bisphenol A, during the thermal curing,<br />
copolymerization <strong>and</strong> homopolymerization do not overlap with each<br />
other. 76 The reactions progress sequentially <strong>and</strong> homopolymerization occurs<br />
only when the copolymerization is completed.<br />
This conclusion is based on the T g –conversion relationship that was<br />
modelled by the DiBenedetto equation. 77 The DiBenedetto equation, Eq.<br />
11.1 is based on the corresponding states.<br />
T g<br />
α<br />
C 1<br />
C 2<br />
T g,α=0<br />
T g<br />
= 1+C 1 α+C 1 α 2 (11.1)<br />
Glass transition temperature<br />
Conversion<br />
Constant, characteristic for the system<br />
Constant, characteristic for the mobility of the repeating units<br />
In a modified diallyl bisphenol A/diaminodiphenylsulfone/bismaleimide<br />
resin, the different temperature regimes were characterized by IR<br />
spectroscopy. The major crosslinking occurs below 150°C. At 190°C the<br />
maleimide moiety is converted into succinimide. 78
Bismaleimide Resins 425<br />
Cure Reaction Pathways. In a homopolymerized bismaleimide resin<br />
system, the maleimide ring addition is the only observable reaction with<br />
conventional methods. When the maleimide is cured in the presence of<br />
an amine, the Michael addition of the amine to the maleimide ring can be<br />
observed.<br />
In solution, using special reagents <strong>and</strong> conditions, a ring-opening<br />
aminolysis reaction has been observed. Such a reaction has been postulated<br />
as a curing mechanism for bismaleimides.<br />
It has been verified that such an aminolysis reaction, accompanied<br />
by ring opening, occurs to a significant extent during the cure of a neat BMI<br />
resin. This partial structure can remain in the network even after a hightemperature<br />
postcure treatment. The existence of the amide product has<br />
been demonstrated in bismaleimide resin formulations selectively labelled<br />
with 13 C atoms <strong>and</strong> 15 N atoms. 79<br />
Cure Kinetics <strong>and</strong> Mechanism. Maleimide reacts with allylphenols in<br />
an ene reaction via an intermediate Wagner-Jauregg reaction, followed by<br />
a Diels-Alder reaction. 80, 81 The Wagner-Jauregg reaction is essentially a<br />
Diels-Alder addition of BMI to the ene adduct of BMI <strong>and</strong> the allylphenol.<br />
The reaction shows a strong dependency on the electron density of the<br />
BMI. The Diels-Alder reaction is facilitated by an increased electrophilicity<br />
of the dienophile. However, a reverse trend is observed for the Wagner-Jauregg<br />
reaction. Therefore, it was concluded that this reaction could<br />
follow a mechanism different from the conventional Diels-Alder reaction,<br />
although the final product looks the same as in the Diels-Alder reaction. 82<br />
In a mixture of 4,4 ′ -bis(maleimido)diphenylmethane <strong>and</strong> 2,2 ′ -diallyl-bisphenol<br />
A (BMDM/DABPA) <strong>and</strong> other models, it was established that<br />
the cure mechanism consists of a combination of step-wise <strong>and</strong> chain polymerization<br />
<strong>and</strong> polycondensation reactions: 83<br />
1. Step-wise ene addition reaction of allyl group to maleimide,<br />
(shown in Figure 11.12).<br />
2. Chain polymerization of the maleimide <strong>and</strong> the propenyl groups<br />
generated by first reaction.<br />
The chain polymerization is the main crosslinking reaction. The<br />
mechanism of the reaction involving monofunctional model compounds<br />
differs from the curing of the actual system because of steric hindrances in<br />
2,2 ′ -diallyl bisphenol A, which retard reversible Diels-Alder reactions, <strong>and</strong>
426 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
OH<br />
O<br />
OH<br />
O<br />
+<br />
N<br />
N<br />
O<br />
O<br />
O<br />
OH<br />
O<br />
N<br />
O<br />
N<br />
O<br />
O<br />
N<br />
O<br />
O<br />
O<br />
OH<br />
O<br />
N<br />
O<br />
N<br />
O<br />
O<br />
N<br />
O<br />
O<br />
N<br />
Figure 11.12: Ene Reaction of Allylphenol <strong>and</strong> Maleimide, Followed by<br />
Wagner-Jauregg Reaction <strong>and</strong> a Diels-Alder Reaction
Bismaleimide Resins 427<br />
different reactivity of maleimide groups. 84 Another mechanism of crosslinking<br />
is the dehydration reaction of phenol groups. The dehydration of<br />
phenolic groups necessarily involves the 1:1 adduct of maleimide <strong>and</strong> allyl<br />
function as a reactant. 85<br />
The homopolymerization of maleimide groups proceeds autocatalytically<br />
under the action of free radicals generated by thermal decomposition<br />
of maleimide propenyl groups donor-acceptor pairs. The steric hindrance<br />
in 2,2 ′ -diallyl-bisphenol A prevents the reversible Diels-Alder reaction.<br />
The methylated analog of 2,2 ′ -diallyl bisphenol A shows a higher<br />
reactivity in thermal free-radical polymerization. 86 The curing kinetics of<br />
bismaleimide modified with diallyl bisphenol A has been modelled by an<br />
autocatalytic <strong>and</strong> n th -order model. 87<br />
Microwave Curing. A comparative study between thermal <strong>and</strong> microwave<br />
curing of bismaleimide resin was done. The degree of cure was<br />
determined with differential scanning calorimetry. No difference in the<br />
chemical reactions taking place during the microwave cure <strong>and</strong> the thermal<br />
cure was detected. Samples that were cured with a conventional oven<br />
showed slightly higher glass transition temperatures than the microwavecured<br />
samples at higher conversions. 88<br />
11.3.2.3 Photo Curing<br />
N-alkylmaleimides homopolymerize in the absence of a photoinitiator<br />
when exposed to UV light in solvents bearing a labile hydrogen. 89 Since<br />
the maleimide is a chromophore, it is considered a photoinitiator together<br />
with a co-initiator. A co-initiator may be methyldiethanolamine, trimethylolpropane<br />
trismercaptopropionate, or poly(ethylene glycol).<br />
Maleimide/vinyl ether systems belong to electron donor/electron acceptor<br />
monomers. Maleimide acts as an electron acceptor <strong>and</strong> the vinyl<br />
ether acts as an electron donor. With stoichiometric maleimide-vinyl ether<br />
mixtures, the reaction proceeds within seconds upon UV exposure. 90 The<br />
initiation reaction is shown in Figure 11.13.<br />
The initiator radicals are formed by hydrogen abstraction from the<br />
excited maleimide molecules. Highly crosslinked polymer networks can<br />
be obtained.<br />
The molecular structure of bismaleimides is quite rigid because of<br />
the presence of aromatic rings. The presence of the aromatic rings, as well
428 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
H<br />
C<br />
C<br />
N R<br />
C C<br />
H<br />
O<br />
CH 2 CH O CH 2 R’<br />
hν<br />
O<br />
H<br />
C*<br />
N R<br />
H C<br />
H<br />
O<br />
CH 2 CH O CH* R’<br />
Figure 11.13: Photoinitiation in Donor Acceptor Systems 91<br />
as the resultant high crosslinked density during thermal curing, give the<br />
cured product its high heat-resistance, resulting in a high T g <strong>and</strong> a high<br />
mechanical strength.<br />
For the radiation curing of bismaleimides, comonomers such as<br />
2,2 ′ -diallyl bisphenol A <strong>and</strong> 4-hydroxybutylvinyl ether have been tested.<br />
Unlike N-alkylmaleimide <strong>and</strong> N-phenylmaleimide, BMI does not react<br />
with vinyl ether without a photoinitiator. Triphenylphosphine oxide is a<br />
suitable photoinitiator.<br />
2,2 ′ -Diallyl bisphenol A, which is a good property modifier for BMI<br />
in thermal curing formulation, does not polymerize with either BMI or<br />
4-hydroxybutylvinyl ether, even in the presence of a photoinitiator. However,<br />
2,2 ′ -diallyl bisphenol A is a co-initiator <strong>and</strong> speeds up the reaction of<br />
a ternary system. 91<br />
11.3.2.4 Anionic Initiators<br />
Several maleimides can be polymerized by nanometer sized Na + /TiO 2<br />
initiators. The temperature for the polymerization initiated by nanometer<br />
sized Na + /TiO 2 is lower than that for the radical polymerization. An anionic<br />
mechanism resulting from the catalysis by Na + /TiO 2 as the counter<br />
ion is proposed.<br />
92, 93<br />
11.3.2.5 Diels-Alder Polymerization<br />
A monomer suitable for Diels-Alder polymerization is shown in Figure<br />
11.14. The reaction between α,α ′ -dibromo-m-xylene (DBMX) <strong>and</strong><br />
sodium 1,2,3,4,5-pentamethylcyclopenta-1,3-dienide gives the respective<br />
pentamathylcyclopentadiene derivative, 25 as depicted in Figure 11.14.
Bismaleimide Resins 429<br />
CH 3<br />
CH 3<br />
H 3 C<br />
CH 3<br />
H 3 C<br />
CH 2<br />
Br CH 2<br />
Br<br />
CH 3<br />
CH 3 CH 3<br />
CH 3<br />
CH 3<br />
H 3 C<br />
CH 3<br />
Na +<br />
Na +<br />
H 3 C CH 3 CH 2 CH<br />
CH 3 2<br />
H 3 C CH 3 H 3 C<br />
CH 3<br />
CH 3<br />
Figure 11.14: Synthesis of Bis-1,3-methyl-1,2,3,4,5-pentamethylcyclopenta-<br />
2,4-diene benzene<br />
The Diels-Alder polymerization is shown in Figure 11.15. The reaction<br />
must be performed in dimethylformamide at 140 to 150°C because<br />
of the low solubility of the BMI.<br />
11.3.3 Interpenetrating Networks<br />
11.3.3.1 Polyurethane Bismaleimide<br />
In polyurethane/poly(urethane-modified bismaleimide-bismaleimide) interpenetrating<br />
polymer networks (PU/P(UBMI-BMI) IPNs) interpenetration<br />
occurs at the hard segment domains of PU, which leads to an enhancement<br />
of the phase separation of PU. The dispersing tendency of the dispersed<br />
phase increases. 94<br />
Poly(butylene adipate)-based polyurethane-crosslinked epoxy (BMI/<br />
PU-EP IPN) <strong>and</strong> bismaleimide from interpenetrating networks are prepared<br />
by using the simultaneous bulk polymerization technique. It was<br />
demonstrated that the bismaleimide was dissolved primarily in the polyurethane<br />
domains of the epoxy matrix to form a compatible system, thereby<br />
increasing the mechanical strength of the BMI/PU-EP IPNs.<br />
95, 96<br />
An epoxy based on poly(propylene oxide) has a better grafting effect
430 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
H 3 C<br />
CH 3 CH 2<br />
CH 3<br />
CH<br />
CH 3 2<br />
O<br />
O<br />
H 3 C<br />
CH 3<br />
CH 3<br />
H 3 C<br />
N R N<br />
CH 3 CH 3 O O<br />
CH 3 CH 2 CH<br />
CH 3 2<br />
O<br />
O<br />
N<br />
O<br />
O<br />
N<br />
Figure 11.15: Diels-Alder Polymerization<br />
due to higher compatibility between the BMI than poly(butylene adipate)<br />
epoxies. 97<br />
The incorporation of chain-extended BMI into polyurethane-modified<br />
epoxy systems increases the thermal stability, <strong>and</strong> tensile <strong>and</strong> flexural<br />
properties, but decreases the impact strength <strong>and</strong> the glass transition temperature.<br />
98<br />
11.3.3.2 Unsaturated Polyester Bismaleimide<br />
A bismaleimide resin monomer can be readily dissolved in the uncured<br />
polyester matrix up to a concentration of about 20%. 99 Spectroscopic investigation<br />
during curing indicates that the crosslinking process is strongly<br />
affected by the presence of the bismaleimide in the system. The maleimide<br />
groups react preferentially with the styrene. The styrene radical reacts<br />
with both the unsaturated polyester <strong>and</strong> the maleimide moieties so that a<br />
crosslinked structure can emerge. When the maleimide groups are fully<br />
consumed, the curing proceeds as in a neat resin. The bismaleimide effects<br />
an increase of the crosslinking density of the final product. Further, the<br />
bismaleimide increases the overall stiffness of the network.
Bismaleimide Resins 431<br />
11.4 PROPERTIES<br />
In comparison to epoxy resins, BMI resins exhibit a higher tensile strength<br />
<strong>and</strong> modulus, excellent chemical <strong>and</strong> corrosion resistance, better dimensional<br />
stability, <strong>and</strong> good performances at elevated temperature.<br />
11.4.1 Thermal Properties<br />
Among two high temperature adhesives, based on epoxy <strong>and</strong> bismaleimide,<br />
the bismaleimide-based adhesive shows a better high temperature performance<br />
<strong>and</strong> is more resistant to thermal aging than an epoxy based resin. 100<br />
There are relationships between structure <strong>and</strong> thermal properties of polymers.<br />
101<br />
11.4.2 Water Sorption<br />
In general, a disadvantage of thermoset resins is their tendency to absorb<br />
significant amounts of water when exposed to humid environments. The<br />
absorbed moisture has detrimental effects on material performance. The<br />
temperature dependence of moisture content in equilibrium is controversial.<br />
It has been reported that the equilibrium moisture content is independent<br />
of temperature, 102 but also that it is dependent on the temperature.<br />
103, 104<br />
From the viewpoint of thermodynamics, the temperature dependence<br />
of the solubility is governed by the enthalpy of dissolution<br />
d lnc s<br />
d1/T = −∆H s/R. (11.2)<br />
During hydrothermal cycling experiments, the molecular network structure<br />
of BMI appears to change. 105, 106 It was concluded that in the course<br />
of water absorption at elevated temperatures, a chemical degradation can<br />
occur. This is part of an aging mechanism. IR spectra obtained by the<br />
reflection technique during water absorption show that the b<strong>and</strong> at 1600<br />
cm −1 increases. 107 This b<strong>and</strong> is attributed to the N − H stretching of an<br />
amine <strong>and</strong> also of an amide. The hydrolysis reaction is shown in Figure<br />
11.16. It is assumed that the hydrolysis is similar to the reverse reaction of<br />
formation of a bismaleimide. 107 When a BMI resin was stored in water at<br />
temperatures of up to 70°C for a period of 18 months, blistering <strong>and</strong> severe<br />
microcracking occurred, leading to severe weakening of the materials. 103
432 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
O<br />
N<br />
H 2 O<br />
O<br />
O<br />
OH<br />
N<br />
H<br />
H 2 O<br />
O<br />
O<br />
OH<br />
H<br />
OH N<br />
H<br />
Figure 11.16: Hydrolysis of a Cured Bismaleimide Resin<br />
The presence of about 10 to 15% of alkenyl-substituted cyanate in<br />
dicyanate <strong>and</strong> bismaleimide blends leads to a marked reduction in moisture<br />
absorption in comparison with an unmodified bismaleimide/cyanate blend<br />
containing a comparable amount of bismaleimide.<br />
The modified samples display thermal stabilities that are indistinguishable<br />
from cured resins that have not undergone immersion. 108 The<br />
moisture transport can be correlated to the glass transition temperature <strong>and</strong><br />
the network properties. The network structure can be systematically varied<br />
by the initial monomer composition <strong>and</strong> the conditions of curing. 109<br />
11.4.2.1 Multivariate Analysis<br />
An analysis of samples subjected to accelerated ageing tests shows that<br />
simple near infrared spectroscopic measurements on virgin materials can<br />
predict results otherwise obtained from dynamic mechanical thermal analysis,<br />
<strong>and</strong> can provide correlations with thermogravimetric analysis.<br />
Therefore, a rapid screening method for multivariate analysis has<br />
been proposed, in conjunction with a combinatorial approach for the development<br />
of advanced composites. 110
Bismaleimide Resins 433<br />
11.4.3 Recycling<br />
Various styrene copolymers containing comonomers with a pendant furan<br />
ring were subjected to Diels-Alder reactions with a monomaleimide or a<br />
bismaleimide. When the materials are heated in the presence of excess of<br />
2-methylfuran, the retro Diels-Alder reaction is induced. The process is<br />
rather a trans Diels-Alder reaction. The maleimides are released with the<br />
furanic additive. Concomitantly the original copolymers can be recovered.<br />
The reaction is of interest because of the possibility of recycling crosslinked<br />
polymers by a simple thermal treatment. 111<br />
11.5 APPLICATIONS AND USES<br />
11.5.1 Biochemical Reagents<br />
Bismaleimides are used as reagents in biochemical investigations. 112 Bismaleimide<br />
is used as a crosslinking reagent for the synthesis of bifunctional<br />
antibodies. The use of a solid-phase reactor in the preparation of the<br />
bifunctional antibodies eliminates many time-consuming separation steps<br />
between fragmentation <strong>and</strong> conjugation steps. 113<br />
11.6 SPECIAL FORMULATIONS<br />
11.6.1 Adhesives<br />
For high-temperature usage, i.e., above 200°C, either bismaleimides or<br />
polyimides are suitable. These are supplied as films, with or without a<br />
carrier. Epoxies are not generally used at temperatures beyond 150°C, although<br />
there are some modified epoxies that can be used up to 200°C. 114<br />
11.6.1.1 Void Control<br />
Polyimides have a higher service temperature than bismaleimides. However,<br />
bismaleimides offer some advantages as they do not generate volatiles<br />
during cure. When volatiles are created during curing a high void content<br />
in the adhesive can develop. There are several methods to control the voids.<br />
These include 114<br />
• Vacuum release technique. The joint to be bonded is placed in<br />
an oven under vacuum. The temperature is increased in order to
434 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
reduce the viscosity of the adhesive. When the vacuum is released,<br />
the voids collapse to a negligible volume.<br />
• Another method uses an autoclave where hydrostatic pressure can<br />
be applied. The hydrostatic pressure compresses the gas in a void<br />
<strong>and</strong> reduces its volume.<br />
11.6.1.2 Thermally Reversible Adhesives<br />
A formulation of thermally reversible adhesives consists of a diepoxy compound<br />
<strong>and</strong> aliphatic diamines. The diepoxy compound is formed by the<br />
Diels-Alder reaction between epoxy-containing furans <strong>and</strong> a bismaleimide.<br />
The epoxy resin is cured with aliphatic diamines. 115 At temperatures<br />
above 90°C the retro Diels-Alder reaction occurs, which leads to a significant<br />
loss in the shear modulus. The loss of the shear modulus is reversible<br />
with temperature. Therefore, the formulation can act as a thermally reversible<br />
adhesive. The adhesive bonds are easily broken at elevated temperature<br />
where the modulus is low.<br />
11.6.1.3 Adhesion Improvement<br />
In order to improve the adhesion of Kevlar ∗ fibers to a 2,2-bis[4-(4-maleimido<br />
phenoxy)phenyl]propane (BMPP) resin, the surface of the fibers can<br />
be chlorosulfonated. The fibers are immersed in a solution of chlorosulfonic<br />
acid in dichloromethane at −10°C. After the chlorosulfonation, the<br />
surface concentration of carbon decreases. In the subsequent reaction with<br />
ethylene diamine, allylamine, the O/N ratio again decreases. On the other<br />
h<strong>and</strong>, the O/N ratio was increased by hydrolysis treatment.<br />
The interfacial shear strength (IFSS) is determined by pull-out experiments<br />
of the fiber from the matrix calculated by the relationship<br />
τ = F dL . (11.3)<br />
τ Interfacial shear strength<br />
F Pull-out force<br />
d Diameter of the fiber<br />
L Embedded length of the resin<br />
The interfacial shear strength (IFSS) between Kevlar fibers <strong>and</strong> the<br />
BMPP resin increases slightly due to the chemical treatment.<br />
116, 117<br />
In<br />
∗ Kevlar is a trademark of DuPont company
Bismaleimide Resins 435<br />
graphite/bismaleimide composites, the treatment with ammonia has been<br />
shown to be promising for the improvement of adhesion. 118<br />
11.6.2 Phosphazene-triazine <strong>Polymers</strong><br />
Polyquinoline/bismaleimide blends are miscible thermosetting polymers.<br />
Thermogravimetry shows a 5% weight loss between 450 <strong>and</strong> 535°C for<br />
thin films at 5 to 60% of bismaleimide loading. The glass transition temperatures<br />
are between 275 <strong>and</strong> 360°C. 119<br />
11.6.3 Phosphazene-triazine <strong>Polymers</strong><br />
Phosphazene-triazine polymers can be obtained by curing a ternary blend<br />
of tris(2-allylphenoxy)triphenoxy cyclotriphosphazene (TAP), tris(2-allylphenoxy)-s-triazine<br />
(TAT) <strong>and</strong> bis(4-maleimidophenyl)methane (BMM).<br />
The maleimide component increases the thermal stability. The tensile<br />
strength decreases <strong>and</strong> the modulus increases with increasing maleimidecontent.<br />
Tensile properties improve for an allyl/maleimide ratio of two. 120<br />
11.6.4 Porous Networks<br />
Network structures have been prepared by in-situ polymerization of a<br />
mixture of N-phenylmaleimide <strong>and</strong> 1,1 ′ -(methylene di-4,1-phenylene)-<br />
bismaleimide in 80% poly(vinylidene difluoride-co-hexafluoropropylene)<br />
(PVDH). The maleimide monomers are forming thermoreversible gels<br />
with PVDH.<br />
After polymerization, porous networks are obtained by removing the<br />
PVDH by solvent extraction. The poly(maleimide) networks are stable up<br />
to 380°C in an inert atmosphere. It is suggested that these networks may<br />
be used for thermally stable membranes. 121<br />
11.6.5 Nonlinear Optical Systems<br />
Thermally stable second-order nonlinear optical polymeric materials based<br />
on bismaleimide contain chromophores with excellent thermal stability,<br />
such as the N-maleimide of Disperse Orange 3. The synthesis of the monomer<br />
is shown in Figure 11.17. A full interpenetrating polymer network<br />
can be formed by the simultaneous reaction of bismaleimide <strong>and</strong> a solgel<br />
process of the alkoxysilane dyes. The dynamic thermal <strong>and</strong> temporal
436 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
O<br />
+<br />
H 2 N N N NO 2<br />
O<br />
O<br />
N<br />
N N NO 2<br />
O<br />
Figure 11.17: Synthesis of the Maleimide of Disperse Orange 3<br />
stabilities of the interpenetrating network are much better than those of<br />
comparable non-interpenetrating networks. 122<br />
Azo chromophores with allyl groups at one or two ends of the<br />
molecules can be thermally cured with bis(maleimidodiphenyl)methane to<br />
give crosslinked <strong>and</strong> chromophore-modified bismaleimide resins. The resins<br />
show no appreciable decomposition up to 300°C. By incorporating<br />
a chromophore into the network of a BMI resin, an improvement of the<br />
thermal stability of the materials is achieved. 123<br />
Examples of azo chromophore allyl compounds include (4-(N,Ndiallyl)-4<br />
′ -nitrophenyl)azoaniline, allyl-4-[(4-N-allyl-N-ethyl)aminophenylazo]-α-cyanocinnamate,<br />
<strong>and</strong> allyl-4-[(4-N,N-diallyl)aminophenylazo]-<br />
α-cyanocinnamate, c.f. Figure 11.18.
Bismaleimide Resins 437<br />
CH 2 CH 2<br />
CH CH<br />
H<br />
N CH 2 C 2<br />
NO 2<br />
CH 2<br />
CH 3 CH<br />
H 2 C<br />
N CH 2<br />
CH 2 CH 2<br />
CH CH<br />
H 2 C<br />
N CH 2<br />
N<br />
N<br />
N<br />
N<br />
N<br />
N<br />
CH<br />
C CN<br />
C O<br />
O<br />
CH 2<br />
CH<br />
CH 2<br />
CH<br />
C CN<br />
C O<br />
O<br />
CH 2<br />
CH<br />
CH 2<br />
Figure 11.18: Azo Chromophore Allyl Compounds: (4-(N,N-Diallyl)-4 ′ -nitrophenyl)azoaniline,<br />
allyl-4-[(4-N-Allyl-N-ethyl)aminophenylazo]-α-cyanocinnamate,<br />
allyl-4-[(4-N,N-Diallyl)amino-phenylazo]-α-cyanocinnamate
438 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
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108. I. Hamerton, H. Herman, K. T. Rees, A. Chaplin, <strong>and</strong> S. J. Shaw. Water uptake<br />
effects in resins based on alkenyl-modified cyanate ester-bismaleimide<br />
blends. Polym. Int., 50(4):475–483, April 2001.<br />
109. J. E. Lincoln, R. J. Morgan, <strong>and</strong> E. E. Shin. Moisture absorption-network<br />
structure correlations in BMPM/DABPA bismaleimide composite matrices.
446 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
J. Adv. Mater., 32(4):24–34, October 2000.<br />
110. I. Hamerton, H. Herman, A. K. Mudhar, A. Chaplin, <strong>and</strong> S. J. Shaw. Multivariate<br />
analysis of spectra of cyanate ester/bismaleimide blends <strong>and</strong> correlations<br />
with properties. Polymer, 43(11):3381–3386, May 2002.<br />
111. C. Gousse, A. G<strong>and</strong>ini, <strong>and</strong> P. Hodge. Application of the Diels-Alder reaction<br />
to polymers bearing furan moieties. 2. Diels-Alder <strong>and</strong> retro-Diels-<br />
Alder reactions involving furan rings in some styrene copolymers. Macromolecules,<br />
31(2):314–321, January 1998.<br />
112. R. Fronzes, S. Chaignepain, K. Bathany, M. F. Giraud, G. Arselin, J. M.<br />
Schmitter, A. Dautant, J. Velours, <strong>and</strong> D. Brethes. Topological <strong>and</strong> functional<br />
study of subunit h of the F 1 F 0 ATP synthase complex in yeast saccharomyces<br />
cerevisiae. Biochemistry, 42(41):12038–12049, October 2003.<br />
113. B. S. DeSilva <strong>and</strong> G. S. Wilson. Synthesis of bifunctional antibodies for<br />
immunoassays. Methods, 22(1):33–43, September 2000.<br />
114. L. F. M. da Silva, R. D. Adams, <strong>and</strong> M. Gibbs. Manufacture of adhesive<br />
joints <strong>and</strong> bulk specimens with high-temperature adhesives. Int. J. Adhes.<br />
Adhes., 24(1):69–83, February 2004.<br />
115. J. H. Aubert. Thermally removable epoxy adhesives incorporating thermally<br />
reversible Diels-Alder adducts. J. Adhes., 79(6):609–616, June 2003.<br />
116. T. K. Lin, B. H. Kuo, S. S. Shyu, <strong>and</strong> S. H. Hsiao. Improvement of the adhesion<br />
of kevlar fiber to bismaleimide resin by surface chemical modification.<br />
J. Adhes. Sci. Technol., 13(5):545–560, 1999.<br />
117. T. K. Lin, S. J. Wu, J. G. Lai, <strong>and</strong> S. S. Shyu. The effect of chemical<br />
treatment on reinforcement/matrix interaction in kevlar-fiber/bismaleimide<br />
composites. Composites Science <strong>and</strong> Technology, 60(9):1873–1878, July<br />
2000.<br />
118. M. Pegoraro, L. Di L<strong>and</strong>ro, <strong>and</strong> F. Severini. Interfacial phenomena, adhesion<br />
<strong>and</strong> macroscopic properties in polymer composites. Macromol. Symp.,<br />
139:13–30, April 1999.<br />
119. H. S. Nalwa, M. Suzuki, A. Takahashi, A. Kageyama, Y. Nomura, <strong>and</strong><br />
Y. Honda. High performance polyquinoline/bismaleimide miscible blends.<br />
Chem. Mat., 10(9):2462–2469, September 1998.<br />
120. C. P. Reghunadhan Nair <strong>and</strong> K. N. Ninan. Phosphazene-triazine polymers<br />
by alder-ene reaction. Polym. Polym. Compos., 12(1):55–62, 2004.<br />
121. P. Jannasch. Porous polymaleimide networks. J. Mater. Chem., 11(9):<br />
2303–2306, 2001.<br />
122. R. J. Jeng, C. C. Chang, C. P. Chen, C. T. Chen, <strong>and</strong> W. C. Su. Thermally<br />
stable crosslinked nlo materials based on maleimides. Polymer, 44(1):<br />
143–155, January 2003.<br />
123. J. D. Luo, C. M. Zhan, <strong>and</strong> Z. G. Qin. Bismaleimide resins modified by bior<br />
tri-allyl-functionalized azo chromophores for second-order optical nonlinearity.<br />
React. Funct. Polym., 44(3):219–225, July 2000.
12<br />
Terpene Resins<br />
Terpenes are widespread in nature, mainly in plants as constituents of essential<br />
oils. Some terpenes are pure hydrocarbons, but there are also terpenes<br />
with hydroxyl functions <strong>and</strong> carbonyl functions. Terpenes provide<br />
plants <strong>and</strong> flowers with fragrance.<br />
12.1 HISTORY<br />
Polyterpene resins were discovered in 1789 when turpentine was treated<br />
with sulfuric acid to produce a crude resin. Turpentine is a semi-fluid resin<br />
obtained from pines. Turpentine is used as a thinner, antiseptic, drug,<br />
pesticide, insecticide, <strong>and</strong> raw material for the chemical industry.<br />
Rouxeville observed that a great number of hydrocarbons may be<br />
changed in their composition so that an artificial product that is formed is<br />
distinguished by a new composition. This occurs by oxidation or polymerization.<br />
He patented a process of polymerization by treatment with sulfuric<br />
acid. 1, 2<br />
12.2 MONOMERS<br />
Terpenes <strong>and</strong> related monomers are relatively non-toxic liquids that may<br />
be obtained from natural renewable nonpetroleum sources. The structure<br />
of terpenes can be essentially derived from isoprene. This fact is known as<br />
the isoprene rule. The terpene unit consists of two isoprene units. There-<br />
447
448 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
CH 3<br />
CH 3<br />
CH 3<br />
CH 2<br />
CH 3<br />
CH 3<br />
CH 3<br />
α-Pinene<br />
β-Pinene<br />
Limonene<br />
Figure 12.1: Terpenes<br />
fore, terpenes have the general molecular formulas (C 5 H 8 ) 2n . According<br />
to the number of isoprene units, terpenes are classified into monoterpenes<br />
(2 isoprene units), sesquiterpenes (3 isoprene units), diterpenes (4 isoprene<br />
units), triterpenes (6 isoprene units), <strong>and</strong> tetraterpenes (8 isoprene units).<br />
Polyterpene resins are low molecular weight hydrocarbon polymers<br />
prepared by cationic polymerization or copolymerization of monoterpenes<br />
such as α-pinene <strong>and</strong> β-pinene or limonene. These types of terpenes are<br />
bicyclic terpene hydrocarbons. The structures of some terpenes are shown<br />
in Figure 12.1. α-Pinene <strong>and</strong> β-pinene <strong>and</strong> limonene are liquid at room<br />
temperature. Naturally occurring terpene compounds are shown in Table<br />
12.1. Natural rubber, or poly(isoprene), is a polyterpene which consists of<br />
up of 1000 to 5000 isoprene units.<br />
12.2.1 Resin<br />
Crude resin is obtained by tapping living pine trees. It is a thick, sticky, but<br />
still fluid material. Due to occluded moisture, the material is milky-gray<br />
in color. The resin contains a certain amount of forest debris, such as pine<br />
needles, insects, etc.<br />
The separation of resin into its component parts, namely rosin <strong>and</strong><br />
turpentine, involves two basic operations: cleaning <strong>and</strong> distillation.<br />
The approximate composition of crude resin, as it is received at the<br />
plant for processing, is 70% rosin, 15% turpentine, <strong>and</strong> 15% debris <strong>and</strong><br />
water.<br />
In the first stage of refinement, the resin is diluted with turpentine<br />
<strong>and</strong> heated. During purification by filtering of the hot diluted resin, all<br />
extraneous materials, both solid <strong>and</strong> soluble are removed. Filtration is usu-
Terpene Resins 449<br />
Table 12.1: Naturally Occurring Terpene Compounds<br />
Monoterpenes<br />
α-Pinene In oil of turpentine<br />
β-Pinene<br />
Limonene In various vegetable oils<br />
Camphene<br />
Myrcene In various vegetable oils<br />
Terpinene<br />
Terpinolene<br />
Phell<strong>and</strong>rene In eucalyptus oil<br />
Chrysanthemol<br />
Allo-ocimene<br />
3<br />
Carene<br />
Dipentene<br />
Sesquiterpenes<br />
Longifolene<br />
Carophyllene<br />
Diterpenes<br />
Retinol<br />
Abietic acid<br />
Pimaric acid<br />
Triterpenes<br />
Betulin<br />
Lupeol<br />
Squalene<br />
Polyterpenes<br />
Natural rubber<br />
Guttapercha<br />
From Himalaya pine<br />
Rare, but its provitamin β-carotine is widespread<br />
In rosin<br />
A mixture of rosin acids. Components of pine rosin<br />
In birch bark<br />
In lupin seeds<br />
In shark liver, <strong>and</strong> natural oils
450 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 12.2: Global Production Data (2000) of Terpenes <strong>and</strong> Derivatives 4<br />
Terpene<br />
Mill. Metric tons<br />
Rosin 1.20<br />
Rosin gum 0.72<br />
Turpentine 0.33<br />
Turpentine gum 0.10<br />
ally followed by a washing step. The purified resin then undergoes a steam<br />
distillation.<br />
12.2.2 Turpentine<br />
Turpentine is a clear, flammable liquid, with a pungent odor <strong>and</strong> a bitter<br />
taste. It is immiscible with water <strong>and</strong> has a boiling point above 150°C.<br />
Turpentine is a mixture of organic compounds, mainly terpenes, <strong>and</strong><br />
its composition can vary considerably according to the species of pine from<br />
which it is derived. Fractional distillation of turpentine allows the isolation<br />
of α-pinene <strong>and</strong> β-pinene.<br />
12.2.3 Rosin<br />
Rosin is the major product obtained from pine resin. It remains behind as<br />
the non-volatile residue after distillation of the turpentine <strong>and</strong> is a brittle,<br />
transparent, glassy solid.<br />
It is insoluble in water but soluble in many organic solvents. 4 It<br />
consists mainly of a mixture of abietic acids <strong>and</strong> pimaric acids. Most rosin<br />
is used in a chemically modified form rather than in the raw state in which<br />
it is obtained.<br />
12.2.4 Production Data of Important Monomers<br />
Global production data of the most important monomers used for unsaturated<br />
polyester resins are shown in Table 12.2. Major producers are The<br />
People’s Republic of China, Indonesia, Russia, Brazil, <strong>and</strong> Portugal.
Terpene Resins 451<br />
H 3 C C + CH 3<br />
CH 3<br />
CH 3<br />
H<br />
CH 3<br />
Figure 12.2: Cationic Initiation of the Polymerization of Terpenes<br />
12.3 CURING<br />
12.3.1 Homopolymers<br />
<strong>Polymers</strong> are produced by the cationic polymerization of α-pinene, β-<br />
pinene, or limonene. The initiation reaction is shown in Figure 12.2. The<br />
initial stage is the same for α-pinene <strong>and</strong> β-pinene. However, the subsequent<br />
propagation differs.<br />
β-Pinene <strong>and</strong> limonene contain vinyl double bonds <strong>and</strong> vinylidene<br />
double bonds that facilitate polymerization. α-Pinene does not contain<br />
such double bonds. This makes the chain propagation more difficult for α-<br />
pinene.<br />
β-Pinene <strong>and</strong> limonene resins are manufactured by the reaction in<br />
an aromatic solvent such as xylene or toluene by a Lewis acid, such as<br />
anhydrous aluminum chloride as catalyst. Ethylaluminum dichloride is<br />
also a suitable catalyst. 5<br />
For α-pinene a co-catalyst is needed to reach a degree of polymerization<br />
higher than dimer. Alkyl silicon halides <strong>and</strong> antimony chloride are<br />
suitable co-catalysts. 6–8 The polymers are different in structure <strong>and</strong> molecular<br />
weight, which has a direct effect on the areas of application.<br />
The cationic polymerization is performed at 30 to 60°C, with 1 to<br />
3% AlCl 3 in a solvent. The reaction is strongly exothermic. The reaction<br />
is then quenched with water, dilute alkali, or acid.<br />
The organic phase is washed with water to remove hydrochloric acid<br />
<strong>and</strong> catalyst residues. Then the solvent <strong>and</strong> lower molecular weight dimer<br />
oils are stripped until a material with the desired softening point is obtained.
452 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
12.3.2 Copolymers<br />
Copolymers of α-pinene, β-pinene, limonene, styrene, piperylene, cyclopentadiene,<br />
<strong>and</strong> vinyl toluene can be prepared. The monomers are copolymerized<br />
with Lewis acid catalysts.<br />
The copolymerization of terpenes with other monomers such as styrene<br />
extends their Hildebr<strong>and</strong> solubility parameter. Such copolymers are<br />
compatible with poly(butadiene) rubbers. This copolymer is used in the<br />
manufacture of disposable diapers.<br />
12.3.3 Terpene Phenolic Resins<br />
Terpene phenol resins are used in a variety of applications including adhesive<br />
<strong>and</strong> ink formulations <strong>and</strong> in the manufacture of engineering thermoplastics.<br />
Commercial terpene phenol resins are typically produced by<br />
reacting a terpene with a phenol in a suitable solvent in the presence of a<br />
catalyst. After the reaction is substantially complete, the catalyst is deactivated<br />
with water or clay, <strong>and</strong> the resin is isolated from the reaction mass<br />
product by distillation to remove the solvent <strong>and</strong> by-products.<br />
In particular, a phenol-terpene-cyclic polyolefin resin can be synthesized<br />
by reacting a phenol, a terpene or a low molecular weight propylene<br />
polymer <strong>and</strong> a cyclic polyolefin in the presence of a Friedel-Crafts catalyst<br />
in an aromatic, naphthenic, or paraffinic hydrocarbon solvent.<br />
The monomer compounds can first be blended together, after which<br />
the catalyst is added in small amounts with stirring. This method is particularly<br />
suitable if relatively small amounts of phenol compound have to<br />
be incorporated. The phenolic copolymer may also be prepared according<br />
to a reverse cationic polymerization in a solvent. “Reverse” means that an<br />
activated complex is first formed between the catalyst <strong>and</strong> the phenol compounds<br />
<strong>and</strong> after that the remaining monomer units are added. This method<br />
makes it possible to incorporate higher proportions of phenol compounds.<br />
Both methods can be applied with or without a solvent. By using a solvent,<br />
the reaction can proceed at lower temperatures. 9<br />
12.3.3.1 Carene Resins<br />
Carenes show a poor reactivity. Therefore, an improved procedure has<br />
been identified. For preparation of carene-phenol resins a phenol with a<br />
carene is reacted two steps. The first step comprises reacting the entire
Terpene Resins 453<br />
CH 3<br />
CH 3<br />
CH 3<br />
H<br />
H<br />
H<br />
H 3 C<br />
CH 3<br />
H<br />
H 3 C<br />
CH 3<br />
H<br />
H 3 C<br />
CH 3<br />
H<br />
(+)-2-Carene<br />
(+)-3-Carene<br />
(+)-4-Carene<br />
Figure 12.3: Carenes<br />
amount of phenol with about one-half the amount of carene in the presence<br />
of a catalyst. Then the rest of the carene is reacted with the condensation<br />
product obtained in the first step in the presence of the catalyst. The resulting<br />
phenol-carene resin is then reacted with a reactive terpene to give an<br />
improved resin. 10<br />
Terpene-phenol-aldehyde resins based on α-pinene, phenol, <strong>and</strong> additional<br />
formaldehyde have a high softening point, greater than 140°C. 11<br />
Manufacturing of terpene-phenol resins with low softening points,<br />
i.e., softening points in the range from about 80°C to about 110°C, is very<br />
difficult. The traditional methods for producing such resins use one of two<br />
approaches.<br />
In the first approach, diluents such as mineral oil or polyolefin oligomers<br />
are added to resins having higher softening points. This approach<br />
usually results in reduced adhesive or ink formulation performance or excessive<br />
amounts of volatiles in the resulting resin.<br />
The second approach is to synthesize the low softening point resin<br />
directly. Generally, the synthetic methods in current use produce base resins<br />
that cannot be finished to softening points below 110 °C without leaving<br />
substantial amounts of process solvents or phenol in the resin. Again,<br />
this results in decreased adhesive or ink formulation performance. 12<br />
A terpene phenol-based resin with a low softening point comprises<br />
the reaction of a phenol dissolved in an organic solvent with terpene <strong>and</strong><br />
an acyclic monounsaturated olefin, such as a mixture of 1-diisobutylene<br />
<strong>and</strong> 2-diisobutylene in the presence of a Lewis acid catalyst, such as boron<br />
trifluoride. 13 Boron trifluoride is used as an acetic complex. 10<br />
Cyclic polyolefins can produce products with unacceptable amounts
454 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
of low molecular weight fractions. The low molecular weight fractions<br />
tend to volatilize or cause smoking during the preparation <strong>and</strong> use of hot<br />
melt adhesives. Therefore, the reaction product is washed <strong>and</strong> distilled to<br />
remove the solvent <strong>and</strong> any unreacted phenol. Further, the product may<br />
be sparged with an inert gas at a temperature up to 260°C to remove any<br />
remaining low molecular weight terpene phenol alkylates <strong>and</strong> terpene-terpene<br />
dimers. A high yield of relatively low softening point terpene phenol<br />
resin is produced. It has softening point in the range from about 70°to<br />
about 110°C.<br />
Terpene phenol resins with low melting points are not suitable for<br />
use in printing ink applications. For use in printing inks, the amount of<br />
vinyl aromatic units should be less than 5%. The small fraction of resin<br />
results in good solubility of the resin (in the ink) <strong>and</strong> an effective drying of<br />
the ink. In these types of applications, dicyclopentadiene may be used. 9<br />
Terpene phenolic resins are suitable for more polar adhesive resins.<br />
They are made by the addition of a terpene to phenol.<br />
12.3.4 Terpene Maleimide Resins<br />
Resinous terpene maleimides are useful as tackifiers for elastomers. They<br />
are prepared by reacting equimolar amounts of non-conjugated monocyclic<br />
terpenes <strong>and</strong> maleic anhydride at temperatures between 140°C <strong>and</strong> 200°C.<br />
Iodine in amounts of 0.05% to 0.15% is used as catalyst.<br />
In the first step, maleic adducts with the terpene are formed, including<br />
both mono adducts <strong>and</strong> a minor amount of di-adducts. This adduct<br />
mixture is reacted with stoichiometric amounts of an aliphatic primary diamine,<br />
such as ethylene diamine. A terpene maleimide resin having an<br />
average molecular weight between about 500 Dalton <strong>and</strong> about 600 Dalton<br />
is recovered. 14<br />
A suitable terpene type is the terpene fraction containing about 90%<br />
terpinolene with the remainder being monocyclic terpene hydrocarbons<br />
<strong>and</strong> terpene alcohols.<br />
A certain procedure 14 yields a product, which is a resinous terpene<br />
maleimide, with properties as summarized in Table 12.3. The terpene<br />
imide resins are soluble in aromatic hydrocarbons, chlorinated hydrocarbons,<br />
esters, ketones, ethers, <strong>and</strong> alcohols, but insoluble in aliphatic<br />
hydrocarbons. Due to their molecular weight <strong>and</strong> compatibility (as shown<br />
by cloud point of 160°C), the resins find utility as tackifiers in chemically
Terpene Resins 455<br />
Table 12.3: Properties of a Resinous Terpene Maleimide<br />
Property<br />
Unit<br />
Softening point 88 [°C]<br />
Acid number 1 [mgKOH/g]<br />
Number-average molecular weight 533 [Dalton]<br />
Cloud point 159 [°C]<br />
polar formulations. The terpene imides prepared are compounded with<br />
vinyl acetate-ethylene copolymers <strong>and</strong> a paraffin wax.<br />
12.4 PROPERTIES<br />
12.4.1 Solubility<br />
Low molecular weight terpene resins have an excellent solubility in elastomers.<br />
This makes them useful for adhesives.<br />
12.4.1.1 Hildebr<strong>and</strong> Solubility Parameters<br />
The Hildebr<strong>and</strong> solubility parameters δ can be predicted on the basis of<br />
the solubility of polymers in solvents with known Hildebr<strong>and</strong> solubility<br />
parameters.<br />
The Hildebr<strong>and</strong> solubility is defined as the square root of the cohesive<br />
energy density, which is a characteristic for the intermolecular interactions<br />
in a pure liquid or solid. The solubility parameter is related to the<br />
heat of mixing H m in Eq. 12.1.<br />
∆H m = n s V s Φ p (δ s − δ p ) 2 (12.1)<br />
H m Heat of mixing<br />
n s Moles of solvent<br />
V s Molar volume of solvent<br />
Φ p Volume fraction of polymer<br />
δ s Solubility parameter of solvent<br />
δ p Solubility parameter of polymer<br />
∆G m decreases as ∆G m decreases. Therefore, if the two Hildebr<strong>and</strong><br />
solubility parameters approach one another, the heat of mixing approaches<br />
a minimum. The theory of solubility parameters was developed<br />
by Scatchard in 1931 <strong>and</strong> further refined by Hildebr<strong>and</strong>. 15
456 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Terpene resins will be effective as solid solvents for an elastomer<br />
when their Hildebr<strong>and</strong> solubility parameters are close to the Hildebr<strong>and</strong><br />
solubility parameters of the respective polymer. For example, from Table<br />
12.4 it can be seen that pure polyterpene resins are suitable tackifiers<br />
for poly(ethylene), natural rubber, <strong>and</strong> poly(butadiene) polymers. Further,<br />
terpene phenol resins are suitable tackifiers for poly(vinyl acetate), poly-<br />
(methyl methacrylate), <strong>and</strong> poly(ethylene terephthalate).<br />
12.4.2 Adhesive Properties<br />
12.4.2.1 Tackifiers<br />
Low molecular weight polyterpene resins are addressed as tackifiers. They<br />
act as solid solvents for adhesive backbone polymers <strong>and</strong> can modify the<br />
ability of an adhesive formulation in wetting a surface. The resins impart a<br />
tack, as they modify certain adhesion characteristics.<br />
The adhesive properties are expressed in terms of shear adhesion,<br />
peel adhesion, <strong>and</strong> quick stick. Quick stick is the resistance to separation<br />
of the adhesive from substrate, bonded without pressure.<br />
The addition of the rosin ester to ethylene/vinyl acetate (EVA) copolymers<br />
produces a compatible mixture, whereas for a terpene resin a less<br />
compatible mixture is obtained. The increase in the vinyl acetate amount<br />
in the EVA decreases the crystallinity of EVA. Both the storage <strong>and</strong> the<br />
loss moduli decrease, but the peel strength <strong>and</strong> the immediate adhesion increase.<br />
The immediate adhesion of the EVA/tackifier blends is affected by<br />
both the compatibility <strong>and</strong> the rheological properties of the blends. An increase<br />
in the VA content increases the flexibility of the adhesives <strong>and</strong> thus<br />
a decrease in peel strength is obtained. 16<br />
The tackifying properties are used not only for adhesive purposes.<br />
For example, the cover material of a golf ball can consist of an ionomer<br />
resin with up to 50% of a tackifier such as terpene resins, or rosin ester<br />
resins. 17<br />
12.4.2.2 Cotackifiers<br />
Polyterpene resins are compatible with paraffins. Therefore, they are also<br />
compatible with petroleum hydrocarbon resins that are used as cotackifiers.<br />
Other cotackifiers include rosins <strong>and</strong> coumarone-indene resins.
Terpene Resins 457<br />
Table 12.4: Hildebr<strong>and</strong> Solubility Parameters δ of Solvents <strong>and</strong> <strong>Polymers</strong><br />
18, 19 Solvent δ<br />
MPa 1/2 a<br />
n-Pentane 14.4<br />
n-Hexane 14.9<br />
Diethyl ether 15.4<br />
1,1,1-Trichloroethane 15.8<br />
Turpentine 16.6<br />
Cyclohexane 16.8<br />
Xylene 18.2<br />
Ethyl acetate 18.2<br />
Benzene 18.7<br />
Methylethylketone 19.3<br />
Acetone 19.7<br />
Pyridine 21.7<br />
Ethanol 26.2<br />
Dimethyl sulfoxide 26.4<br />
n-Butanol 28.7<br />
Methanol 36.2<br />
Water 48.0<br />
Polymer<br />
δ<br />
MPa 1/2<br />
Poly(ethylene) 16–17<br />
Poly(butadiene) 16–17<br />
Poly(styrene) 17–20<br />
Poly(vinyl acetate) 19<br />
Poly(methyl methacrylate) 19–26<br />
Poly(ethylene terephthalate) 19-22<br />
Rosin esters 18<br />
β-Pinene polyterpene 16<br />
Terpene phenol polymers 19–21<br />
a MPa 1/2 ∼ = 2.05× µm
458 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 12.5: Important Specifications of Terpene Resins<br />
Parameter<br />
Solubility<br />
Cloud point<br />
Softening point<br />
Toluene insolubles<br />
Color<br />
Viscosity at compounding temperatures<br />
Thermal stability<br />
Compatibility<br />
Remarks<br />
Ring <strong>and</strong> ball method<br />
Residues from catalyst<br />
Gardner scale<br />
12.4.3 Characterization<br />
Some important specifications of terpene resins are shown in Table 12.5.<br />
12.4.3.1 Rheological <strong>and</strong> Aging Characteristics<br />
Polyterpene resins can modify the rheological <strong>and</strong> aging characteristics of<br />
adhesive backbone polymers. In this way the polymers themselves become<br />
usable as adhesives. It is possible to correlate rheological characteristics to<br />
the tack, shear, <strong>and</strong> peel.<br />
12.4.3.2 Cloud Point<br />
Higher molecular weight resins will have a higher cloud point in polymerpolymer<br />
combinations.<br />
12.4.3.3 Softening Point<br />
The softening point is related to the glass transition temperature <strong>and</strong> to the<br />
melt viscosity. Polyterpene resins have cyclic <strong>and</strong> polycyclic structures<br />
in the backbone. These provide high softening points at low molecular<br />
weights <strong>and</strong> low viscosities, which is very useful. Terpene resins are available<br />
in softening points from 25°C to 135°C. Most commercial resins have<br />
softening points of 85°C to 115°C.<br />
12.4.3.4 Color<br />
The color of a resin is monitored in a 50% heptane solution <strong>and</strong> is given in<br />
the Gardner scale.
Terpene Resins 459<br />
12.4.3.5 Toluene Insolubles<br />
The toluene insolubles is a measure of the amount of inorganic material in<br />
the resin. The toluene insolubles consist mainly of catalyst residues.<br />
12.4.4 Recycling<br />
12.4.4.1 Pyrolysis of Poly(isoprene)<br />
Controlled thermal depolymerization at 300 to 380°C of cis-1,4-poly(isoprene)<br />
produces a liquid poly(isoprene) having a considerably lower molecular<br />
weight in comparison to the starting cis-1,4-polymer. The product is<br />
enriched in trans-1,4-units <strong>and</strong> 3,4-units together with vinylidene units.<br />
FT-IR spectroscopy shows that the end groups of liquid poly(isoprene)<br />
consist of diene, triene <strong>and</strong> tetraene moieties. Aldehyde groups conjugated<br />
with dienes <strong>and</strong> trienes are also analyzed.<br />
Pyrolysis opens a possible low cost source of raw materials, since the<br />
pyrolysis of natural <strong>and</strong> synthetic cis-1,4-poly(isoprene) produces mainly<br />
dipentene (DL-limonene) with small amounts of isoprene <strong>and</strong> other products.<br />
A 3,4-poly(isoprene)-rich polymer produces mainly dipentene. The<br />
residual of pyrolysis consists of 3,4-poly(isoprene). The crude dipentene<br />
obtained from cis-1,4-poly(isoprene) pyrolysis can be converted into a terpene<br />
resin usable in adhesive formulations <strong>and</strong> as thermoplastic rubber<br />
tackifier. 20<br />
12.4.4.2 Biodegradation<br />
Films for packaging based on isotactic poly(propylene)-modified with natural<br />
terpene resins are biodegradable. It was found that a certain microbial<br />
community was able to erode the blend films but not the plain isotactic<br />
poly(propylene) film. 21<br />
12.5 APPLICATIONS AND USES<br />
Only three terpenes, i.e., α-pinene, β-pinene, <strong>and</strong> limonene have found<br />
commercial application in the manufacture of polyterpene resins. Polyterpene<br />
resins are used as pressure-sensitive adhesives, hot-melt adhesives,<br />
<strong>and</strong> sealants. Some polyterpene resins are used in chewing gum.
460 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
12.5.1 Sealants<br />
12.5.1.1 Moisture Barrier Films<br />
Oriented poly(propylene) (OPP) is known for its inherent moisture barrier<br />
properties. However, certain applications require even greater resistance to<br />
water vapor transmission to increase the shelf life of the packed material.<br />
The incorporation of terpene polymers at low levels in high crystallinity<br />
poly(propylene) provides a product film having significantly improved<br />
moisture barrier properties. The addition of a terpene polymer increases<br />
the extent of amorphous orientation in the stretching of the poly-<br />
(propylene), thereby restricting the diffusion of water molecules. 3 Terpene<br />
polymers can also be added to poly(propylene) film materials to improve<br />
the heat seal properties.<br />
12.5.2 Pressure-sensitive Adhesives<br />
Pressure-sensitive adhesives are used for adhesive tapes <strong>and</strong> labels. The<br />
substrates include paper, polyvinyl chloride, polyester, poly(propylene), or<br />
cellophane. 22<br />
Pressure-sensitive adhesives (PSA) can be prepared via hot melts,<br />
solvents, <strong>and</strong> waterborne systems. In solvent-containing systems, formulations<br />
with a high content of solid material are possible, requiring a<br />
minimum solvent recovery. Mixtures of polyterpene resins with different<br />
molecular weights can be used to establish the desired adhesive properties.<br />
12.5.2.1 Hot-melt Extrusion<br />
The production of PSA via hot-melt extrusion methods is the preferred<br />
route. The corresponding rubber is a styrene isoprene rubber or a styrene<br />
butadiene rubber. These block copolymers are elastomers, but become<br />
thermoplastic upon heating.<br />
12.5.2.2 Waterborne Systems<br />
For waterborne applied systems, the structural polymer <strong>and</strong> the tackifying<br />
resin must be supplied as dispersion. No solvent recovery system is<br />
necessary. For waterborne systems, the manufacture via rosin esters is easier<br />
than the emulsification of polyterpene resins. For carboxylated styrene
Terpene Resins 461<br />
butadiene rubber, pure polyterpenes are suitable. For neoprene <strong>and</strong> acrylic<br />
rubbers, terpene phenol polymers are used.<br />
12.5.2.3 Styrene-isoprene Block copolymers<br />
Poly(styrene-b-isoprene-b-styrene) (SIS)/tackifier resin blends show a<br />
lower critical solution temperature phase transition at around 150°C <strong>and</strong> an<br />
upper critical solution temperature phase transition at around 200°C. The<br />
properties of the pressure-sensitive adhesive in SIS/tackifier resin blends<br />
change with the annealing temperature. 23<br />
12.5.3 Polyacrylate Hot-melt Pressure-sensitive Adhesives<br />
For industrial pressure-sensitive adhesive (PSA) tape applications it is very<br />
common to use polyacrylate PSAs. Polyacrylates possess a variety of advantages<br />
over other elastomers. They are highly stable toward UV light,<br />
oxygen, <strong>and</strong> ozone. Synthetic <strong>and</strong> natural rubber adhesives normally contain<br />
double bonds, which make these adhesives unstable to environmental<br />
effects. Further advantages of polyacrylates include their transparency <strong>and</strong><br />
their serviceability within a relatively wide temperature range.<br />
Polyacrylate PSAs are generally prepared in solution by free-radical<br />
polymerization. A variety of polymerization methods are suitable for<br />
preparing low molecular mass PSAs. Chain transfer agents, such as alcohols<br />
or thiols, can be used. These chain transfer agents reduce the molecular<br />
weight <strong>and</strong> broaden the molecular weight distribution.<br />
Another controlled polymerization method is that of atom transfer<br />
radical polymerization (ATRP). The initiators include monofunctional or<br />
difunctional secondary or tertiary halides <strong>and</strong>, for abstracting the halides,<br />
complexes of certain metals. However, the metal catalysts have the side<br />
effect of adversely influencing the aging of the PSAs (gelling, transesterification).<br />
Unfortunately, the majority of metal catalysts are toxic, discolor<br />
the adhesive, <strong>and</strong> can be removed from the polymer only by means<br />
of complicated precipitations. Another method is to use a nitroxide-controlled<br />
polymerization process. It is possible to realize high conversions in<br />
combination with high molecular weight <strong>and</strong> low polydispersity.<br />
In order to increase the cohesion, the polymer is crosslinked. Curing<br />
takes place thermally, by UV crosslinking, or by electron beam curing.<br />
The polyacrylates are normally applied to the corresponding backing<br />
material from solution using a coating bar, <strong>and</strong> then dried. However,
462 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
it is difficult to produce PSA tapes with a high adhesive application rate,<br />
without bubbles. One solution to overcome this disadvantage is the hotmelt<br />
process. In this process, the PSA is applied to the backing material<br />
from the melt.<br />
Polyacrylate hot-melt pressure-sensitive adhesives with copolymerized<br />
photoinitiators <strong>and</strong> with a narrow molecular weight distribution can<br />
be processed very effectively in a melt process <strong>and</strong> can be crosslinked very<br />
efficiently by UV crosslinking. 24 For the use of the polymers as pressure-sensitive<br />
adhesives, they are optimized by blending with tackifying<br />
resins. Tackifying resins include pinene resins, indene resins, <strong>and</strong> rosins,<br />
<strong>and</strong> derivatives.<br />
12.5.4 Hot-Melt Adhesives<br />
Hot-melt adhesives are commonly used in bookbindery, for the manufacture<br />
of packaging, for coatings, diapers, other sanitary products, <strong>and</strong> tapes.<br />
Due to their properties, polyterpene resins are ideal materials for the formulation<br />
of hot melt systems.<br />
They are compatible with many structural polymers <strong>and</strong> they exhibit<br />
a high softening point together with a low melt viscosity. Therefore,<br />
upon melting, a low viscous mixture with the structural polymer is formed.<br />
Therefore, polyterpene resins are considered as the best modifiers to improve<br />
the tack <strong>and</strong> adhesion of elastomeric systems. Limonene polymers<br />
have a good hot tack performance. Most commonly used hot-melt mixtures<br />
are EVA (or block copolymers), resin tackifier, <strong>and</strong> wax blends.<br />
Most commercially available hot melt adhesives require temperatures<br />
of above 180°C to ensure complete melting of all the components<br />
<strong>and</strong> also to achieve a satisfactory application viscosity. Adhesive formulations<br />
that can be applied at temperatures below 120°C are prepared using<br />
low molecular weight components or a high wax content, however, the<br />
application viscosity <strong>and</strong> adhesive properties suffer.<br />
Softer or more amorphous components may be added in order to<br />
improve adhesion. However, these components reduce the effective heat<br />
resistance.<br />
Modified rosins <strong>and</strong> modified terpenes, having a molecular weightto-softening<br />
point ratio of less than about 10, when used as tackifier alone<br />
or in combination, in a hot melt provide adhesives that can be applied at<br />
low temperature <strong>and</strong> exhibit high heat resistance <strong>and</strong> good cold resistance.
Terpene Resins 463<br />
A modified rosin or terpene is a phenolic-modified resin. 25 The molecular<br />
weight-to-softening point ratio is the molecular weight of the modified<br />
rosin or modified terpene in Dalton divided by its softening point in °C.<br />
12.5.5 Coatings<br />
Thermoplastic resin compositions consisting of a poly(phenylene ether)<br />
(PPE) <strong>and</strong> polyamide (PA) resin show outst<strong>and</strong>ing properties that make<br />
them well suited for inline coating. They also find extensive use in external<br />
automobile components. They are used with paints such as acrylic<br />
urethane paint, acrylic amino paint, <strong>and</strong> polyester polyol paint, but these<br />
paints do not show sufficient adhesion to the PPE/PA resin composition,<br />
<strong>and</strong> when they are used for direct coatings, peeling of the coating film may<br />
occur. For this reason, the main method used is to first apply a coat of<br />
primer to the molded product, followed by a finish coat. However, with<br />
the tendency towards cutting costs, attitudes towards coatings tend to shift<br />
toward the primerless approach, <strong>and</strong> there is a changeover toward thinner<br />
coating films.<br />
When a specified terpene phenol resin is added to a PPE/PA resin<br />
composition, the coating film adhesion of the composition can be considerably<br />
improved. 26<br />
The terpene phenol resin must have a hydroxyl value of 50 or greater.<br />
If the hydroxyl value is too low, the adhesion will be poor. For example,<br />
a suitable terpene phenol resin is a copolymer of limonene <strong>and</strong> phenol or<br />
copolymer of α-pinene <strong>and</strong> phenol. It has an average molecular weight of<br />
700 Dalton, a softening point of 120 to 150°C, <strong>and</strong> a hydroxyl value of 50<br />
to 130 mgKOH/g.<br />
12.5.6 Sizing Agents<br />
Sizing agents are used by the paper industry to give paper <strong>and</strong> paperboard<br />
some degree of resistance to wetting <strong>and</strong> penetration by aqueous liquids.<br />
There are two basic categories of sizing agents: acid <strong>and</strong> alkaline. Acid<br />
sizing agents are intended for use in acid papermaking systems, traditionally<br />
less than pH 5. Analogously, alkaline sizing agents are intended for<br />
use in alkaline papermaking systems, typically at a pH greater than 6.5.<br />
Most acid sizing agents are based on rosin. The development of<br />
sizing with a rosin-based size is dependent upon its reaction with papermaker’s<br />
alum, Al 2 (SO 4 ) 3 × 14 − 18H 2 O. Since aluminum species that ex-
464 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
ist predominantly at a low pH (< pH 5) are required for the appropriate<br />
interactions needed to effect sizing, rosin <strong>and</strong> alum have been used primarily<br />
in acid papermaking systems.<br />
It has been shown that, by proper selection of addition points in the<br />
papermaking system. By using cationic dispersed rosin sizes, rosin-based<br />
sizes can be used in papermaking systems up to about pH 7, thus extending<br />
the range of acid sizes. However, due to the limitations imposed by alum<br />
chemistry, the efficiency of rosin-based sizes decreases above about pH<br />
5.5. 8<br />
12.5.6.1 Alkaline Sizing<br />
Sizing agents developed for papermaking systems above pH 6.5 are generally<br />
based on alkylketene dimer (AKD) or alkenyl succinic anhydride<br />
(ASA).<br />
Alkylketene dimer. Sizes based on alkylketene dimer (AKD) form covalent<br />
bonds with cellulose to give proper orientation <strong>and</strong> anchoring of the<br />
hydrophobic alkyl chains. This covalent bond formation makes AKD sizing<br />
very efficient <strong>and</strong> resistant to strong penetrants. However, AKD sizes<br />
have some limitations: small changes in the amount of size added can lead<br />
to large differences in sizing (steep sizing response curve), <strong>and</strong> there is a<br />
slow rate of sizing development (cure).<br />
Alkenyl succinic anhydride. The other major alkaline sizing agent is<br />
based on ASA. As with AKD, the development of sizing with ASA sizes<br />
is also dependent on the formation of covalent bonds with cellulose to give<br />
proper orientation <strong>and</strong> anchoring. ASA is more reactive than AKD, resulting<br />
in a greater sizing effect. However, the reaction rate with water is<br />
also greater, producing a hydrolyzate that is an inefficient sizing agent in<br />
alkaline systems. It also contributes to the formation of deposits on the<br />
papermaking machine. To minimize the formation of hydrolyzate, ASA is<br />
typically emulsified at the mill immediately before addition to the papermaking<br />
system.<br />
Cationic resins. Cationic resins have been used in the papermaking process.<br />
8 Sizing of paper can be done with an aqueous emulsion of a partially<br />
saponified terpene resin, 1 to 5% alum, <strong>and</strong> optionally a partially saponified
Terpene Resins 465<br />
rosin. Sizing in the absence of alum is achieved with an aqueous dispersion<br />
of fortified rosin, a hydrocarbon resin <strong>and</strong> a vinyl imidazoline polymer as a<br />
retention aid. Another sizing composition for paper comprises an aqueous<br />
dispersion of partially neutralized rosin, a terpene polymer, <strong>and</strong> 1 to 5%<br />
aluminum sulfate.<br />
The addition of a cationic polyamine resin is used to anchor the rosin<br />
to the paper pulp. The cationic polyamine resin is of the type polyalkyleneamine-epihalohydrin<br />
resin. 8 High levels of size or cationic resin cause<br />
no significant reduction in the papers coefficient of friction.<br />
12.5.7 Toner Compositions<br />
Toner compositions containing copolymers based on styrene <strong>and</strong> myrcene<br />
can be synthesized by an anionic polymerization process. The reaction<br />
needs dried reagents. A resin was obtained with a T g of 60°C, with M n of<br />
36 kDalton <strong>and</strong> M w of 64 kDalton. Charge additives are quaternary ammonium<br />
bisulfates <strong>and</strong> distearyl methyl hydrogen ammonium bisulfate. 27<br />
12.5.8 Chewing Gums<br />
In general, chewing gums <strong>and</strong> bubble gums utilize as their gum base a combination<br />
of natural or synthetic elastomers. Preferably, polymers of limonene<br />
or other dipentenes with rosin-glycerol esters are used in the formulation<br />
of chewing gums. The gum base that is selected provides the chewing<br />
gum with its masticatory properties. A chewing gum base is normally admixed<br />
with sugars or synthetic sweeteners, perfumes, flavors, plasticizers,<br />
<strong>and</strong> fillers. Then it is milled <strong>and</strong> formed into sticks, sheets, or pellets.<br />
Cottonseed oil is sometimes also added to give the gum softness.<br />
Styrene butadiene rubber (SBR) is a synthetic elastomer that is widely used<br />
as a gum base in chewing gums. However, SBR is not widely used in manufacturing<br />
soft chew gums because it lacks the desired physical properties.<br />
Poly(isobutylene) is widely used in manufacturing soft chew gums even<br />
though it is much more expensive than SBR.<br />
In any case, chewing gum compositions are typically comprised of<br />
a water soluble bulk portion, a water insoluble chewing gum base portion<br />
<strong>and</strong> typically water insoluble flavoring agents. The water soluble portion<br />
dissipates with a portion of the flavoring agent over a period of time during<br />
chewing. The gum base portion is retained in the mouth throughout the<br />
chewing process.
466 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
The gum base includes a number of ingredients that are subject to<br />
deterioration through oxidation during storage. The insoluble gum base<br />
is generally comprised of elastomers, elastomer plasticizers, waxes, fats,<br />
oils, softeners, emulsifiers, fillers, texturizers <strong>and</strong> miscellaneous ingredients,<br />
such as antioxidants, preservatives, colorants, <strong>and</strong> whiteners.<br />
The compounds containing carbon-carbon double bonds, such as<br />
fats, oils, unsaturated elastomers, <strong>and</strong> elastomer plasticizers are susceptible<br />
to oxidation. The gum base commonly contains 15 to 35% by weight<br />
of the chewing gum.<br />
In chewing gum base natural or artificial antioxidants are utilized to<br />
stabilize the rubbery polymer. For instance, β-carotenes, acidulants (e.g.,<br />
Vitamin C), propyl gallate, BHA, <strong>and</strong> BHT are commonly used to stabilize<br />
the rubber used in manufacturing chewing gum. Such antioxidants are<br />
included in the chewing gum base as a stabilizer to inhibit oxidation.<br />
Antioxidants are widely used in food products susceptible to degeneration,<br />
in one form or another, due to oxidation. Commercial applications<br />
include use in processed meat <strong>and</strong> poultry, salad dressings, seasonings,<br />
snacks, nuts, soup bases, edible fats <strong>and</strong> oils, natural foods, pet foods, <strong>and</strong><br />
packaging. In addition to foods, antioxidants have been used to prevent<br />
oxidation in various cosmetic <strong>and</strong> toiletry products <strong>and</strong> in pharmaceutical<br />
preparations. The primary purpose in each of these applications is to<br />
prevent deterioration of desirable product characteristics by inhibiting oxidation.<br />
12.6 SPECIAL FORMULATIONS<br />
12.6.1 Toughener for Novolaks<br />
There is considerable technical interest in hydrophobically substituted, but<br />
nevertheless crosslinkable <strong>and</strong> grindable novolaks, since they have considerably<br />
better compatibility with hydrophobic substrates. In addition, it<br />
is desirable to control the crosslinking rate of novolak/crosslinking agent<br />
mixtures at a given temperature. It is furthermore desirable to reduce the<br />
high brittleness of the crosslinking products of novolaks.<br />
These difficulties can be overcome by means of modified novolaks<br />
which contain, as modifying components, terpenes <strong>and</strong> unsaturated carboxylic<br />
acids or derivatives of these compounds.<br />
Phenols that have at least one free ring hydrogen atom in the orthoor<br />
para-position can be substituted to the phenolic hydroxyl group with
Terpene Resins 467<br />
terpenes in the presence of Lewis or protonic acids. This gives low-molecular-weight<br />
synthetic resins which have a relatively high melting point, but<br />
cannot be crosslinked. However, if a significant number of phenolic hydroxyl<br />
groups is still present after the reaction, terpene modified resins can<br />
be subjected to crosslinking reactions. 28<br />
12.6.2 Fluoro Copolymers<br />
A more uniform copolymer with a narrower molecular weight distribution<br />
for improved flex life can be obtained by the copolymerization of tetrafluoroethylene<br />
(TFE) <strong>and</strong> perfluoro (alkyl vinyl ether) (PAVE) in the presence<br />
of a terpene in an aqueous polymerization medium.<br />
This produces a melt-fabricable TFE/PAVE copolymer (PFA) having<br />
a uniformly distributed PAVE. The small amount of terpene added to the<br />
polymerization system does not decrease the rate of polymerization, but<br />
is present in an amount that is effective for improving the uniformity of<br />
the resin by narrowing the molecular weight distribution, i.e., in the ppm<br />
range. 29<br />
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with natural terpene resins. In H. Insam, N. Riddech, <strong>and</strong> S. Klam-
Terpene Resins 469<br />
mer, editors, Microbiology of Composting, pages 265–272. Springer-Verlag,<br />
Berlin, 2002.<br />
22. D. Satas, editor. H<strong>and</strong>book of Pressure Sensitive Adhesive Technology. Satas<br />
& Associates, Warwick, RI, 3rd edition, 1999.<br />
23. S. Akiyama, Y. Kobori, A. Sugisaki, T. Koyama, <strong>and</strong> I. Akiba. Phase behavior<br />
<strong>and</strong> pressure sensitive adhesive properties in blends of poly(styreneb-isoprene-b-styrene)<br />
with tackifier resin. Polymer, 41(11):4021–4027, May<br />
2000.<br />
24. M. Husemann <strong>and</strong> S. Zollner. UV-crosslinkable acrylic hotmelt PSAs with<br />
narrow molecular weight distribution. US Patent 6 720 399, assigned to tesa<br />
AG (Hamburg, DE), April 13 2004.<br />
25. D. L. Haner, B. Carillo, <strong>and</strong> J. Mehaffy. Hot melt adhesive composition.<br />
US Patent 6 593 407, assigned to National Starch <strong>and</strong> Chemical Investment<br />
Holding Corporation (New Castle, DE), July 15 2003.<br />
26. T. Ohtomo, K. Myojo, <strong>and</strong> H. Kubo. Compositions of polyphenylene ether<br />
<strong>and</strong> polyamide resins containing terpene phenol resins. US Patent 5 554 693,<br />
assigned to General Electric Company (Pittsfiled, MA), September 10 1996.<br />
27. M. K. Georges, N. A. Listigovers, S. V. Drappel, M. V. McDougall, <strong>and</strong><br />
G. R. Allison. Toner compositions with styrene terpene resins. US Patent<br />
5 364 723, assigned to Xerox Corporation (Stamford, CT), November 15<br />
1994.<br />
28. W. Hesse, E. Leicht, <strong>and</strong> R. Sattelmeyer. Modified novolak terpene products.<br />
US Patent 5 096 996, assigned to Hoechst Aktiengesellschaft (DE), March 17<br />
1992.<br />
29. T. Iwasaki <strong>and</strong> M. Kino. Process for manufacture of a copolymer of tetrafluoroethylene<br />
<strong>and</strong> perfluoro (alkyl vinyl ether). US Patent 6 586 546, assigned<br />
to DuPont-Mitsui Fluorochemicals Co. Ltd. (Tokyo, JP), July 1 2003.
13<br />
Cyanoacrylates<br />
Cyanoacrylates were commercially introduced in 1950 by Tennesee Eastman<br />
Company. Cyanoacrylate adhesives are monomeric adhesives. They<br />
are generally quick-setting materials which cure to clear, hard glassy resins,<br />
useful as sealants, coatings, <strong>and</strong> particularly adhesives for bonding<br />
together a variety of substrates. 1 <strong>Polymers</strong> of alkyl 2-cyanoacrylates are<br />
also known as superglues.<br />
13.1 MONOMERS<br />
13.1.1 Synthesis<br />
In 1895 Auwers <strong>and</strong> Thorpe 2 attempted to synthesize diethyl-2,2-dicyanoglutarate<br />
(Figure 13.1) by base-catalyzed condensation of aqueous formaldehyde<br />
<strong>and</strong> ethyl cyanoacetate. They isolated a mixture of oily oligomers<br />
<strong>and</strong> an amorphous polymer of higher molecular weight.<br />
CH 2<br />
CN<br />
C<br />
C O<br />
O<br />
R<br />
R<br />
H<br />
O<br />
CN<br />
C CH 2<br />
C<br />
O<br />
CN<br />
C H<br />
C O<br />
O<br />
R<br />
Figure 13.1: 2,4-Dicyanoglutaric Acid Ester<br />
471
472 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
CH 2<br />
O<br />
+<br />
H<br />
CN<br />
C H<br />
C O<br />
O<br />
R<br />
-H 2 O<br />
CH 2<br />
CN<br />
C<br />
C O<br />
O<br />
R<br />
Figure 13.2: Synthesis of Cyanoacrylates: Knoevenagel Reaction<br />
In fact ethyl 2-cyanoacrylate monomer was synthesized as an intermediate,<br />
which underwent an immediate polymerization reaction. The<br />
condensation of formaldehyde with cyanoacetate is still the most important<br />
method for the commercial production of the monomers, c.f. Figure 13.2.<br />
The reaction mechanism takes place as a base-catalyzed Knoevenagel condensation<br />
of cyanoacetate <strong>and</strong> formaldehyde to give an intermediate 2-substituted<br />
methylol derivative.<br />
A. E. Ardis 3 at B.F. Goodrich (in 1947), found that the polymer-oligomer<br />
mixture obtained in the formaldehyde-cyanoacetate condensation<br />
reaction could be thermally depolymerized with acid catalysts. However,<br />
the monomer prepared by utilizing these methods was unstable <strong>and</strong> the<br />
yields were low. Later 4 it was realized that the water is responsible for<br />
polymerization. Instead of aqueous formaldehyde, paraformaldehyde was<br />
used with an organic solvent to remove the water by azeotropic distillation.<br />
The stability of the monomer can be enhanced by the redistillation of<br />
the crude monomer in the presence of small quantities of acidic stabilizers,<br />
e.g., sulfur dioxide.<br />
Several other methods for cyanoacrylate monomer production have<br />
been described, including the pyrolysis of 3-alkoxy-2-cyanopropionates, 5<br />
transesterification of ethyl 2-cyanoacrylate, 6 <strong>and</strong> displacement of cyanoacrylate<br />
monomer from its anthracene Diels-Alder adduct by treatment<br />
with maleic anhydride. This last method is used for the synthesis of monomers<br />
that are not accessible or may be difficult to prepare by the retropolymerization<br />
route, for example, difunctional cyanoacrylates, 7 thiocyanoacrylates,<br />
8 <strong>and</strong> perfluorinated monomers.<br />
13.1.2 Crosslinkers<br />
To improve the cohesive strength, difunctional monomeric crosslinking<br />
agents may be added to the monomer compositions. These include alkyl
Compound<br />
Cyanoacrylates 473<br />
Table 13.1: Commercially Available Cyanoacrylates<br />
Remarks<br />
Methyl cyanoacrylate Strongest bonding to metals, good stability<br />
against solvents<br />
Ethyl cyanoacrylate General purpose<br />
Allyl cyanoacrylate > 100°C service temperature<br />
n-Butyl cyanoacrylate Flexible, medical applications 9<br />
Isobutyl cyanoacrylate Medical applications 9<br />
2-Octyl cyanoacrylate Medical applications9, 10<br />
2-Methoxyethyl cyanoacrylate<br />
Weak odor<br />
2-Ethoxyethyl cyanoacrylate Weak odor<br />
2-Methoxy-1-methylethyl Weak odor<br />
cyanoacrylate<br />
CH 2<br />
CN<br />
C<br />
C O<br />
R<br />
CH 2<br />
CN<br />
C<br />
C O<br />
R<br />
n<br />
O<br />
O<br />
Figure 13.3: Basic Structure of Cyanoacrylate Monomers <strong>and</strong> <strong>Polymers</strong><br />
bis(2-cyanoacrylates), triallyl isocyanurates, alkylene diacrylates, alkylene<br />
dimethacrylates, 1,1,1-trimethylolpropane triacrylate, <strong>and</strong> alkyl bis-<br />
(2-cyanoacrylates). 11<br />
13.1.3 Commercial Products<br />
Commercial products consist mainly of monofunctional monomers. Commonly<br />
encountered monomers are shown in Table 13.1. The monomers<br />
are usually low-viscosity liquids with excellent wetting properties. The<br />
basic structure of cyanoacrylate monomers <strong>and</strong> polymers is shown in Figure<br />
13.3. The syntheses of the monomers <strong>and</strong> the raw materials are shown<br />
in Figures 13.4 <strong>and</strong> 13.5. Because of the high electronegativity of the<br />
nitrile group <strong>and</strong> the carboxylate groups, they undergo rapid anionic polymerization<br />
on contact with basic catalysts. The anionic polymerization is<br />
facilitated by the possibility of resonance structures as shown in Figure<br />
13.6. The polymers formed in this way exhibit high molecular weights,<br />
usually more than 10 6 Dalton.
474 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
CN<br />
CH 2<br />
O<br />
H<br />
C<br />
H<br />
+ +<br />
C O R<br />
N<br />
O<br />
H<br />
-H2O<br />
N<br />
CN<br />
CH 2 C H<br />
C O R<br />
O<br />
CH 2<br />
CN<br />
C<br />
C O<br />
O<br />
R<br />
Figure 13.4: Synthesis of Cyanoacrylates: Mannich Reaction<br />
Cl<br />
C<br />
H<br />
Cl<br />
C<br />
Cl<br />
H 2 O<br />
Cl 2<br />
CH 3<br />
C<br />
O<br />
O<br />
H<br />
Cl<br />
CH 2<br />
C<br />
O<br />
H<br />
O<br />
Figure 13.5: Synthesis of Chloro acetic acid
Cyanoacrylates 475<br />
Y - +<br />
CH 2<br />
CN<br />
C<br />
C O<br />
O<br />
R<br />
Y<br />
CH 2<br />
C -<br />
CN<br />
C O<br />
O<br />
R<br />
Y<br />
CH 2<br />
C<br />
C<br />
C<br />
O -<br />
N<br />
O<br />
R<br />
Y<br />
CH 2<br />
C -<br />
N<br />
C<br />
C O<br />
O<br />
R<br />
Figure 13.6: Resonance Structures of the Growing Anions<br />
13.2 SPECIAL ADDITIVES<br />
13.2.1 Plasticizers<br />
Adhesives based on cyanoacrylate esters are effective bonding agents for<br />
a wide variety of materials, but do not give a permanent bond in joints involving<br />
glass. A strong bond to glass is obtained initially but generally the<br />
joint fails after a period of weeks or months at room temperature conditions.<br />
The extremely rapid curing rate on glass caused by the basic nature<br />
of the surface is responsible for high stresses that are generated in the bond<br />
line immediately adjacent to the glass, at a molecular level. These stresses<br />
make the polymer in the bond line uniquely susceptible to chemical or<br />
physical degradation. 12<br />
Cyanoacrylate adhesive bonds also tend to be relatively brittle; therefore,<br />
the adhesive compositions are often plasticized. 13 Typical plasticisers<br />
include various alkyl esters <strong>and</strong> diesters <strong>and</strong> alkyl <strong>and</strong> aromatic phosphates<br />
<strong>and</strong> phosphonates, diallyl phthalates <strong>and</strong> aryl <strong>and</strong> diaryl ethers. Plasticisers<br />
are summarized in Table 13.2<br />
For glass bonding, dibutyl phthalate is a suitable plasticizer in n-<br />
butyl cyanoacrylate. 12 The glass bonds were tested for durability by subjecting<br />
them to a sequence of washing cycles in a domestic dishwasher.<br />
The results shown in Table 13.3. suggest that the bond strength decreases<br />
with increasing proportions of plasticizer. Levels greater than about 40%<br />
result in bonds of reduced strength. The concentration of plasticizer needed
476 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 13.2: Plasticizers 11<br />
Compound<br />
Dioctyl phthalate<br />
Dimethyl sebacate<br />
Triethyl phosphate<br />
Tri(2-ethylhexyl)phosphate<br />
Tri(p-cresyl)phosphate<br />
Glyceryl triacetate<br />
Glyceryl tributyrate<br />
Diethyl sebacate<br />
Dioctyl adipate<br />
Isopropyl myristate<br />
Butyl stearate<br />
Lauric acid<br />
Dibutyl phthalate<br />
Trioctyl trimellitate<br />
Dioctyl glutarate<br />
Table 13.3: Durability of Bonds to Glass with Various Amounts of Plasticizer<br />
12 Dibutyl phthalate [%] Bond Strength N/mm 2 Durability a<br />
0 2.70 5<br />
10 3.20 3<br />
20 3.20 5<br />
25 1.94 5<br />
30 2.46 50<br />
40 1.86 90<br />
50 0.80 90<br />
60 0.32 20<br />
70 0.08 10<br />
a No. of Dishwasher Cycles
Cyanoacrylates 477<br />
for good durability is about 30% to 50%.<br />
13.2.2 Accelerators<br />
The esters of 2-cyanoacrylic acid are also commonly called quick-set adhesives,<br />
since they generally harden after a few seconds when used or the<br />
joined parts exhibit at least a certain degree of initial strength. However,<br />
in the case of some substrates, especially acidic substrates such as wood or<br />
paper, the polymerization reaction may be very greatly delayed.<br />
Acidic materials exhibit a pronounced tendency to draw the adhesive,<br />
which is often highly liquid, out of the joint gap by capillary action<br />
before hardening has taken place in the gap.<br />
Even in cases in which, for reasons of geometry, the adhesive must<br />
be applied in a relatively thick layer in the joint gap or in cases where<br />
relatively large amounts of adhesive are applied <strong>and</strong> relatively large drops<br />
of adhesive protrude from between the parts to be joined, rapid hardening<br />
throughout may rarely be achieved. 14<br />
Therefore, attempts have been made to accelerate the polymerization<br />
for such applications by means of certain additives. The methods used may<br />
roughly be divided into three categories:<br />
• Addition of accelerators directly to the adhesive formulation. This<br />
is possible to only a very limited extent, however, since substances<br />
having a basic or nucleophilic action, which would normally<br />
bring about a pronounced acceleration of the polymerization<br />
of the cyanoacrylate adhesive, are generally used at the expense of<br />
the storage stability of such compositions.<br />
• The second common method is the addition of the accelerators<br />
shortly before application of the adhesive in virtually a two-component<br />
system. However, such method has the disadvantage that<br />
the working life is limited after the activator has been mixed in. In<br />
addition, with the small amounts of activator that are required, the<br />
necessary accuracy of metering <strong>and</strong> homogeneity of mixing are<br />
difficult to achieve.<br />
• A third process is the use of activators in the form of a dilute solution.<br />
The solution is either sprayed onto the parts before they<br />
are bonded onto the places where the adhesive is still liquid after<br />
the substrates have been joined. The solvents used for such dilute<br />
solutions of activators are generally low-boiling organic solvents.
478 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
R 1<br />
(CH 2 CH 2 O)n Si O<br />
R 2<br />
n = 4..10<br />
Figure 13.7: Silacrown ethers 15<br />
Cure accelerators include crown ethers, calixarene compounds, silacrown<br />
compounds, <strong>and</strong> amines.<br />
13.2.2.1 Silacrown Compounds<br />
Silacrown compounds as additives give substantially reduced fixture <strong>and</strong><br />
cure times on wood <strong>and</strong> other deactivating surfaces such as leather, ceramic,<br />
plastics <strong>and</strong> metals with chromate treated or acidic oxide surfaces.<br />
Silacrown accelerators have significantly lower reported acute toxicity<br />
than the crown ether compounds. The lower observed toxicity of<br />
silacrowns in comparison to crown-ethers may be related to the hydrolytic<br />
instability of the Si-O-C linkage. Thus, while the silacrown ring is stable in<br />
the cyanoacrylate composition, it will open up in biological environments,<br />
reducing both acute <strong>and</strong> chronic risk. 16<br />
Silacrowns are prepared by transesterification of alkoxysilanes with<br />
poly(ethylene glycol)s, i.e., they are reaction products of silanes but are not<br />
themselves silanes. Silacrown compounds are commercially available <strong>and</strong><br />
are reportedly readily synthesized in good yield. 15–18 Silacrown ethers are<br />
shown in Figure 13.7.<br />
13.2.2.2 Calixarenes<br />
Cyanoacrylate adhesive compositions that employ calixarene compounds<br />
as additives give substantially reduced fixture <strong>and</strong> cure times on wood <strong>and</strong><br />
other deactivating surfaces such as leather, ceramic, plastics <strong>and</strong> metals<br />
with chromate-treated or ceramic oxide surfaces. 19–21
Cyanoacrylates 479<br />
N<br />
S<br />
S<br />
N<br />
HOOC<br />
N<br />
S<br />
S<br />
N<br />
COOH<br />
N<br />
N<br />
S<br />
S<br />
N<br />
N<br />
Figure 13.8: 2,2 ′ -Dipyridyl disulfide, 6,6 ′ -Dithiodinicotinic acid <strong>and</strong> Bis(4-tertbutyl-1-isopropyl-2-imidazolyl)disulfide<br />
13.2.2.3 Amines<br />
Solutions of lower fatty amines, aromatic amines, <strong>and</strong> dimethylamine are<br />
used that are sprayed on the surface before the cyanoacrylate is applied, or<br />
at the same time. Examples are N,N-dimethylbenzylamine, N-methylmorpholine,<br />
<strong>and</strong> N,N-diethyltoluidine.<br />
N,N-Dimethyl-p-toluidine, when subsequently applied to the joined<br />
parts, causes even relatively large amounts of adhesive to harden within<br />
seconds. The poly(cyanoacrylate) so formed is completely free of turbidity.<br />
Disadvantages are the very high volatility of the substance, which does<br />
not permit long waiting times between the application of the accelerator<br />
solution to the substrates to be bonded <strong>and</strong> the subsequent bonding process.<br />
The compound is also toxic. 14<br />
13.2.2.4 Disulfides<br />
Examples of disulfides are dibenzodiazyl disulfide, 6,6 ′ -dithiodinicotinic<br />
acid, 2,2 ′ -dipyridyl disulfide, or bis(4-tert-butyl-1-isopropyl-2-imidazolyl)disulfide,<br />
14 c.f. Figure 13.8.The disulfides have a good accelerating<br />
action, but they nevertheless permit a long waiting time between application<br />
of the activator <strong>and</strong> application of the adhesive. In addition, they avoid<br />
spontaneous, merely superficial hardening.
480 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Compound<br />
Table 13.4: Thickeners<br />
Reference<br />
Fumed silica<br />
16<br />
Poly(cyanoacrylate)<br />
11<br />
Poly(lactic acid)<br />
11<br />
Poly(glycolic acid)<br />
11<br />
Lactic-glycolic acid copolymers<br />
11<br />
Poly(ε-caprolactone)<br />
11<br />
Poly(3-hydroxybutyric acid)<br />
11<br />
Polyorthoesters<br />
11<br />
Polyacrylates<br />
11<br />
Polymethacrylates<br />
11<br />
13.2.3 Thickeners<br />
Thickeners are added to increase the viscosity of 2-cyanoacrylate adhesive<br />
compositions. The 2-cyanoacrylate monomer generally has a low viscosity<br />
of several centipoise, <strong>and</strong>, therefore, the adhesive penetrates into porous<br />
materials such as wood <strong>and</strong> leather or adherents with a rough surface.<br />
Thus, good adhesion bond strengths are difficult to achieve. Thickeners are<br />
summarized in Table 13.4.<br />
Various polymers can be used as thickeners, <strong>and</strong> examples include<br />
poly(methyl methacrylate), methacrylate-type copolymers, acrylic rubbers,<br />
cellulose derivatives, poly(vinyl acetate), <strong>and</strong> poly(2-cyanoacrylate). A<br />
suitable amount of thickener is generally about 20% by weight or less<br />
based on the total weight of the adhesive composition.<br />
Fumed silica for use as thickener is treated with poly(dialkylsiloxane)<br />
or trialkoxyalkylsilanes. 16 The purpose of the silane which is retained<br />
on the surface of the silica is to maintain the fumed silica in a dispersion<br />
within the composition.<br />
13.2.4 Stabilizers<br />
Stabilizers have to be added both for the production <strong>and</strong> for storage. The<br />
stabilizer systems are added so that no polymerization would occur during<br />
transportation <strong>and</strong> storage in sealed drums, even at elevated temperatures<br />
<strong>and</strong> after long periods.<br />
After application polymerization occurs immediately. Accordingly,<br />
besides radical polymerization inhibitors, inhibitors against anionic poly-
Compound<br />
Table 13.5: Stabilizers<br />
Cyanoacrylates 481<br />
Reference<br />
Sulfur dioxide<br />
11<br />
6-Hydroxy-5-[(4-sulfophenyl)azo]-2-naphthalenesulfonic acid<br />
11<br />
Lactone<br />
11<br />
Boron trifluoride<br />
11<br />
Hydroquinone<br />
11<br />
Catechol<br />
11<br />
Pyrogallol<br />
11<br />
p-Benzoquinone<br />
11<br />
2-Hydroxybenzoquinone<br />
11<br />
p-Methoxyphenol<br />
11<br />
tert-Butyl catechol<br />
11<br />
Organic acid<br />
11<br />
Butylated hydroxy anisole<br />
11<br />
Butylated hydroxy toluene<br />
11<br />
tert-Butyl hydroquinone<br />
11<br />
Alkyl sulfate<br />
11<br />
Alkyl sulfite<br />
11<br />
3-Sulfolene<br />
11<br />
Alkylsulfone<br />
11<br />
Alkyl sulfoxide<br />
11<br />
Mercaptan<br />
11<br />
Alkyl sulfide<br />
11<br />
Dioxathiolanes<br />
22<br />
merization are generally added to cyanoacrylate adhesives. Stabilizers are<br />
summarized in Table 13.5.<br />
A typical stabilizer to prevent radical polymerization is hydroquinone.<br />
Boron trifluoride prevents anionic polymerization.<br />
13.2.4.1 Acidic Cation Exchanger<br />
It has been proposed to add a strongly acidic cation exchanger as inhibitor.<br />
Cation exchangers are based on crosslinked poly(styrene)-containing sulfonic<br />
acid groups.<br />
The disadvantage of this approach is that the ion exchanger added<br />
can easily impede the outflow of the adhesive <strong>and</strong> that, as a solid, it does<br />
not act throughout the entire volume of the adhesive.
482 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
13.2.4.2 Acid Groups on Container Walls<br />
It has been proposed to modify the surface of storage containers for cyanoacrylate<br />
adhesives in such a way that they contain acid groups. 23 Although<br />
this proposal can be successfully implemented, it is afflicted by the problem<br />
that the inhibition occurs in the vicinity of the container wall.<br />
13.2.4.3 Sulfur Compounds<br />
Sulfur Dioxide. Another method of stabilizing cyanoacrylate adhesives<br />
is to add sulfur dioxide as an inhibitor. Although this measure has been<br />
successfully applied in practice, it is important to bear in mind that sulfur<br />
dioxide is a gaseous substance <strong>and</strong> that uniform addition is difficult so that<br />
quality variations can occur. In addition, sulfur dioxide can escape from<br />
the adhesive containers by diffusion during storage.<br />
Dioxathiolanes. Cyclic organic sulfates, sulfites, sulfoxides, sulfinates,<br />
for example, 2-oxo-1,3,2-dioxathiolanes, act in raising the ceiling temperature<br />
<strong>and</strong> hence to improve the thermal stability of the adhesives. 22<br />
4,5-Dimethyl-2-oxo-1,3,2-dioxathiolane is a liquid with a boiling<br />
point of 185°C. This is an inhibitor for the anionic polymerization <strong>and</strong><br />
should be effective throughout the entire volume of the adhesive. It could<br />
be added more uniformly <strong>and</strong> more easily than gases. In addition, the discoloration<br />
of the adhesive during storage is prevented. 24<br />
13.2.5 Primers<br />
It is well known in the adhesive field that there are plastic substrates made<br />
from certain types of plastic materials which are extremely difficult to<br />
bond. Such difficult-to-bond materials include low surface energy plastics<br />
such as poly(ethylene) <strong>and</strong> poly(propylene) <strong>and</strong> highly crystalline materials<br />
such as polyacetals <strong>and</strong> poly(butylene terephthalate). As a consequence<br />
of the difficulty in bonding substrates made from these plastics materials<br />
with adhesives, various surface treatments have been employed where such<br />
materials require bonding. Examples of such surface treatments include<br />
corona discharge exposure of the substrate surface, acid etching, plasma<br />
treatment, etc. However, these methods are clearly not applicable to the<br />
bonding of plastic substrates in the domestic or household areas. Alternatively,<br />
various primer compositions have been developed which are de-
Compound<br />
Table 13.6: Primers<br />
Cyanoacrylates 483<br />
Reference<br />
n-Octylamine<br />
25<br />
1,5-Diazabicyclo[4.3.0]non-5-ene<br />
26, 27<br />
1,8-Diazabicyclo[5.4.0]undec-7-ene<br />
26, 27<br />
1,5,7-Triazabicyclo[4.4.0]dec-5-ene<br />
26, 27<br />
Tetra-n-butyl ammonium fluoride<br />
28, 29<br />
Tributylphosphine<br />
30<br />
N,N,N ′ ,N ′ -Tetramethylethylene diamine<br />
31<br />
N,N,N ′ ,N ′ -Tetraethylethylene diamine<br />
32<br />
N,N,N ′ ,N ′ -Tetramethyl-1,3-butane diamine<br />
31<br />
N,N-Dimethyl-N ′ ,N ′ -di(2-hydroxypropyl)-1,3-propane diamine<br />
31<br />
N-2-Aminoethyl-3-aminopropyl-tris(2-ethylhexoxy)silane<br />
31<br />
Imidazole derivatives<br />
33<br />
2-Phenyl-2-imidazoline<br />
33<br />
Organometallic compounds<br />
34<br />
Manganese(III)acetylacetonate<br />
34<br />
N<br />
N<br />
H<br />
N<br />
N<br />
N<br />
N<br />
N<br />
Figure 13.9: 1,5-Diazabicyclo[4.3.0]non-5-ene, 1,8-Diazabicyclo[5.4.0]undec-7-ene<br />
<strong>and</strong> 1,5,7-Triazabicyclo[4.4.0]dec-5-ene<br />
signed to be applied to the plastic substrate to be bonded prior to application<br />
of the adhesive. 31 Primers contain mostly aminic structures. Some<br />
primers are listed in Table 13.6.<br />
13.2.6 Diazabicyclo <strong>and</strong> Triazabicyclo Primers<br />
1,5-Diazabicyclo[4.3.0]non-5-ene, 1,8-Diazabicyclo[5.4.0]undec-7-ene,<br />
<strong>and</strong> 1,5,7-Triazabicyclo[4.4.0]dec-5-ene are shown in Figure 13.9. It is<br />
well known that solutions of amines <strong>and</strong> other organic <strong>and</strong> inorganic bases<br />
will accelerate the curing of cyanoacrylate adhesives. Diazabicyclo <strong>and</strong><br />
triazabicyclo compounds also confer adhesion to nonpolar substrates.<br />
26, 27<br />
This primer acts in a two-component adhesive system comprising<br />
2-cyanoacrylate adhesive <strong>and</strong> the azabicyclo primer. In poly(propylene)
484 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
NH 2<br />
CH 2<br />
CH 2<br />
H<br />
+<br />
N CH 2 CH 2 NH 2 O C (CH 2 ) 10 CH 3<br />
CH 2<br />
CH 2<br />
NH 2<br />
NH<br />
C (CH 2 ) 10 CH 3<br />
CH 2<br />
CH 2<br />
N CH 2 CH 2<br />
CH 2<br />
NH<br />
C (CH 2 ) 10 CH 3<br />
CH 2<br />
NH<br />
C<br />
(CH 2 ) 10 CH 3<br />
Figure 13.10: Condensation of Tris(2-aminoethyl)amine <strong>and</strong> Dodecyl aldehyde 35<br />
the application of 1,8-Diazabicyclo[5.4.0]undec-7-ene, the tensile shear<br />
bond strength raises to up to 74 kg/cm 2 in comparison to 7 kg/cm 2 without<br />
primer.<br />
13.2.7 Polyamine Dendrimers<br />
Compounds with a variety of highly branched architectures are known,<br />
including cascade, dendrimer, hyperbranched, <strong>and</strong> comb-like architectures.<br />
The term multi-amine compounds refers to compounds with such branched<br />
architectures in which branching occurs via tertiary amine groups.<br />
For example, polyamine dendrimers are prepared by the condensation<br />
of tris(2-aminoethyl)amine (TAA) <strong>and</strong> dodecyl aldehyde followed by<br />
the reduction with tetra-n-butylammonium cyanoborohydride. 35 The reaction<br />
is shown in Figure 13.10. The contact between the adhesive <strong>and</strong><br />
the multi-amine compound may be accomplished by mixing immediately<br />
prior to bonding. Ordinarily, however, using the multi-amine compound in
Cyanoacrylates 485<br />
a primer composition will provide the most practical <strong>and</strong> convenient application<br />
to the substrate <strong>and</strong> will give effective bonding improvement on<br />
polyolefin substrates.<br />
13.3 CURING<br />
Cyanoacrylates can be polymerized both by radical <strong>and</strong> by anionic mechanisms.<br />
The polymerization of cyanoacrylates has been monitored by<br />
Raman spectroscopy. 36 Cyanoacrylates polymerize comparatively slowly<br />
with free-radical initiators. However, in the presence of catalytic amounts<br />
of anionic bases <strong>and</strong> in the presence of covalent bases such as amines <strong>and</strong><br />
phosphines, they polymerize extremely rapidly.<br />
The exceptionally fast rate of anionic polymerization of cyanoacrylates<br />
in the presence of a base, including water, made this class of monomers<br />
unique among all acrylic <strong>and</strong> vinyl monomers. Consequently, the anionic<br />
polymerization is initiated by traces of moisture which are to be found on<br />
almost all surfaces. Accordingly, cyanoacrylate adhesives set very quickly<br />
when introduced between two surfaces stored under ambient conditions.<br />
Of the alkyl cyanoacrylate family of monomers, the methyl- <strong>and</strong> ethyl-esters<br />
are used extensively in industrial <strong>and</strong> consumer-type adhesives.<br />
Consequently, most of the published work on the polymerization of cyanoacrylates<br />
focuses on anionic polymerization.<br />
13.3.1 Photo Curing<br />
Although the predominant mechanism by which cyanoacrylate monomers<br />
undergo polymerization is anionic, free-radical polymerization is also<br />
known to occur. Radical polymerization of cyanoacrylate can be achieved<br />
in the presence of a radical forming component <strong>and</strong> a photosensitizer. The<br />
radical generating component can be dibenzoyl peroxide <strong>and</strong> the photoinitiator<br />
component is 2,4,6-triphenylpyrylium tetrafluoroborate (TPT). 37<br />
The chemical structures of these compounds are shown in Figure 13.11.<br />
Some metallocene salts are capable of generating both a cationic species<br />
<strong>and</strong> a free radical species upon exposure to radiation.<br />
Ferrocene <strong>and</strong> DAROCUR 1173 (2-hydroxy-2-methyl-1-phenyl-<br />
1-propane) are photo catalysts suitable for cyanoacrylates. 38 Radiation<br />
times of 5 to 15 seconds are sufficient.
486 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
C<br />
O<br />
O O C<br />
O<br />
O<br />
BF 4<br />
-<br />
Figure 13.11: Dibenzoyl peroxide <strong>and</strong> 2,4,6-Triphenylpyrylium tetrafluoroborate<br />
13.4 PROPERTIES<br />
The particular advantage of cyanoacrylate adhesives in terms of adhesives<br />
technology lies precisely in the high reactivity coupled with the high bond<br />
strengths of the final materials, especially to polar substrates. Due to high<br />
molar mass, good wetting properties, <strong>and</strong> polarity, poly(cyanoacrylate)s<br />
exhibit excellent adhesive properties. In addition, they have been found<br />
useful as polymeric binding agents in controlled drug delivery systems.<br />
They are also useful for dry etching processes.<br />
13.5 APPLICATIONS AND USES<br />
Of the alkyl cyanoacrylate family of monomers, the methyl- <strong>and</strong> ethyl-esters<br />
are used extensively in industrial <strong>and</strong> consumer-type adhesives.<br />
13.5.1 Manicure Composition<br />
Cyanoacrylate compositions are used as manicure compositions in treating<br />
chapped nails. When nails are manicured, it is generally observed that the<br />
moisture content in the nails becomes out of balance or lipids are eluted<br />
out from the nails. As a result, nail chapping proceeds under the manicure<br />
coating. Therefore, the nail chapping can be prevented by adding to manicure<br />
compositions a substance capable of keeping nails in good health or<br />
improving the nail health.<br />
Cyanoacrylates are hardened so quickly that the hardening reaction<br />
thereof is associated with heat generation. Therefore, when cyanoacrylates<br />
are applied to nails, there arises heat irritation. Avocado oil <strong>and</strong> jojoba
Cyanoacrylates 487<br />
oil can be added as plasticizer. In addition, these oils can suppress the<br />
heat generation upon hardening without deteriorating the quick hardening<br />
properties of cyanoacrylates or impairing its storage stability. Furthermore,<br />
these natural oils may prevent nails from keratinization. 39<br />
13.5.2 Tissue Adhesives<br />
The isobutyl, n-butyl, <strong>and</strong> n-octyl cyanoacrylate esters are used clinically<br />
as blocking agents, sealants, <strong>and</strong> tissue adhesives due to their much lower<br />
toxicity as compared with their more reactive methyl <strong>and</strong> ethyl counterparts.<br />
Cyanoacrylate ester compositions can be sterilized using visible light<br />
irradiation at room temperature conditions. 9<br />
There has been a great deal of interest in using tissue adhesives in<br />
many surgical procedures in place of sutures <strong>and</strong> staples for a variety of<br />
reasons, including 40<br />
1. Ease of application <strong>and</strong> reduced clinician time,<br />
2. Location of repairable site as in contoured locations,<br />
3. Biomechanical properties as in weak organs, such as liver <strong>and</strong> pancreas,<br />
<strong>and</strong><br />
4. Minimized hypertrophy <strong>and</strong> scar formation as in plastic surgery.<br />
However, there have been a number of concerns associated with the<br />
alkyl cyanoacrylates. These include<br />
1. Their low viscosity <strong>and</strong> associated difficulties in precise delivery<br />
at the application site in non-medical <strong>and</strong> medical applications,<br />
2. Poor shear strength of the adhesive joint, particularly in aqueous<br />
environments in both medical <strong>and</strong> non-medical applications,<br />
3. High modulus or stiffness of cured polymers at soft tissue application<br />
sites <strong>and</strong> associated mechanical incompatibility, which can<br />
lead to adhesive joint failure <strong>and</strong> irritation of the surrounding tissue,<br />
4. Excessive heat generation upon application of monomers to living<br />
tissue due to exceptionally fast rate of curing resulting in necrosis,<br />
<strong>and</strong><br />
5. Site infection, among other pathological complications, associated<br />
with prolonged residence of the non-absorbable tissue adhesives.
488 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Problems with sterilization may arise. For example, poly(2-octyl<br />
cyanoacrylate), degrades when exposed to a 160°C dry heat sterilization<br />
cycle or 20 to 30 kGy (2 to 3 MRad) of electron beam radiation. 10<br />
13.5.2.1 Bioabsorbable <strong>Polymers</strong><br />
Bioabsorbable polymers have been classified into three groups:<br />
40, 41<br />
• Soluble,<br />
• Solubilizable, <strong>and</strong><br />
• Depolymerizable.<br />
The most common materials used in bioabsorbable implants in orthopaedic<br />
surgery 42 are polyglycolic acid (PGA), polylactic acid (PLA),<br />
<strong>and</strong> polydioxanone (PDS).<br />
Soluble polymers are water-soluble <strong>and</strong> have hydrogen-bonding polar<br />
groups, the solubility being determined by the type <strong>and</strong> frequency of<br />
the polar groups. Solubilizable polymers are usually insoluble salts, such<br />
as calcium or magnesium salts of carboxylic or sulfonic acid-functional<br />
materials which can dissolve by cation exchange with monovalent metal<br />
salts. Depolymerizable systems have chains that dissociate to simple organic<br />
compounds in vivo under the influence of enzymes or chemical catalysis.<br />
Ester of Triethylene glycol. Bioabsorbable tissue adhesives 41, 43 are<br />
based on a methoxypropyl cyanoacrylate as the precursor of an absorbable<br />
tissue adhesive polymer <strong>and</strong> a polymeric, highly absorbable, liquid comprising<br />
an oxalate ester of triethylene glycol as a modifier to modulate the<br />
viscosity of the overall composition, lower the heat of polymerization, <strong>and</strong><br />
increase the compliance <strong>and</strong> absorption rate of the cured adhesive joint.<br />
Copolymers of caprolactone, D,L-lactide, <strong>and</strong> glycolide also are considered<br />
as bioabsorbable.<br />
40, 44<br />
Cyanoacrylate-capped Heterochain <strong>Polymers</strong>. Although the admixture<br />
of a polymeric modifier has been shown to be effective in addressing most<br />
of the medical <strong>and</strong> non-medical drawbacks of cyanoacrylate-based adhesives<br />
represented by methoxypropyl cyanoacrylate, there remain technical<br />
drawbacks in these systems, such as mutual immiscibility of two or more<br />
polymers.
Cyanoacrylates 489<br />
Cyanoacrylate-capped heterochain polymers having two or more<br />
cyanoacrylate ester groups per chain have certain advantages. The heterochain<br />
polymer used for capping can be one or more absorbable polymers<br />
of the following types: polyester, polyester-carbonate, polyether-carbonate,<br />
<strong>and</strong> polyether-ester. The capped polymer can also be derived from a<br />
polyalkylene glycol such as poly(ethylene glycol), or a block copolymer of<br />
poly(ethylene glycol) <strong>and</strong> poly(propylene) glycol.<br />
The capping of the heterochain polymer can be achieved using an<br />
alkyl cyanoacrylate, or an alkoxyalkyl cyanoacrylate such as ethyl cyanoacrylate<br />
or methoxypropyl cyanoacrylate, respectively, in the presence of<br />
phosphorus-based acids or precursors. In fact the capping takes place as<br />
transesterification reaction. In the simplest case, a predried poly(ethylene<br />
glycol) is mixed with ethyl cyanoacrylate in the presence of pyrophosphoric<br />
acid under a dry nitrogen atmosphere. The reaction is allowed to<br />
proceed by heating for 5 hours at 85°C. 40<br />
REFERENCES<br />
1. H. V. Coover, D. W. Dreifus, <strong>and</strong> J. T. O. Conner. Cyanoacrylate adhesives.<br />
In I. Skeist, editor, H<strong>and</strong>book of Adhesives, chapter 27, pages 463–477. Van<br />
Nostr<strong>and</strong> Reinhold, New York, 3rd edition, 1990.<br />
2. K. F. von Auwers <strong>and</strong> J. F. Thorpe. Liebigs Ann. Chem., 285:322, 1895.<br />
3. A. E. Ardis. US Patent 2 467 927, assigned to B. F. Goodrich, New York<br />
(NY), April 19 1949.<br />
4. F. B. Joyner <strong>and</strong> G. F. Hawkins. Method of making α-cyano-acrylates. US<br />
Patent 2 721 858, assigned to Eastman Kodak, Rochester, New York, October<br />
25 1955.<br />
5. A. E. Ardis. Preparation of monomeric alkyl-α-cyano-acrylates. US Patent<br />
2 467 926, assigned to B. F. Goodrich, New York (NY), April 19 1949.<br />
6. A. Vojtkov, K. A. Mager, Y. V. Kokhanov, A. M. Polyakova, <strong>and</strong> Y. B. Vojtekunas.<br />
Method of preparing cyanacrylic acid esters. SU Patent 726 086,<br />
assigned to Inst. Elementoorganicheskikh So. (SU), April 5 1980.<br />
7. C. J. Buck. Modified cyanoacrylate monomers <strong>and</strong> methods for preparation.<br />
US Patent 4 012 402, assigned to Johnson <strong>and</strong> Johnson, (New Brunswick,<br />
NJ), March 15 1977.<br />
8. S. Harris. The preparation of thiocyanoacrylates. J. Polym. Sci., Part. A:<br />
Polym. Chem., 19:2655–2656, 1981.<br />
9. I. N. Askill, S. C. Karnik, <strong>and</strong> R. L. Norton. Methods for sterilizing cyanoacrylate<br />
compositions. US Patent 6 579 916, assigned to MedLogic Global<br />
Corporation (Devon, GB), June 17 2003.
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10. T. Hickey, U. A. Stewart, J. Jonn, <strong>and</strong> J. S. Bobo. Sterilized cyanoacrylate<br />
solutions containing thickeners. US Patent 6 743 858, assigned to Closure<br />
Medical Corporation (Raleigh, NC), June 1 2004.<br />
11. J. C. Leung <strong>and</strong> J. G. Clark. Biocompatible monomer <strong>and</strong> polymer compositions.<br />
US Patent 5 328 687, assigned to Tri-Point Medical L.P. (Raleigh, NC),<br />
July 12 1994.<br />
12. P. F. McDonnell, R. J. Lambert, E. P. Scott, G. M. Wren, <strong>and</strong> M. McGuinness.<br />
Cyanoacrylate adhesive compositions for bonding glass. US Patent<br />
6 607 632, assigned to Loctite (R&D) Limited (Dublin, IE), August 19 2003.<br />
13. L. Corp. Debondable cyanoacrylate adhesive composition. GB Patent<br />
1 529 105, assigned to Loctite Corp, October 18 1978.<br />
14. H. Misiak <strong>and</strong> I. Scheffler. Activator for cyanoacrylate adhesives. US Patent<br />
6 547 917, assigned to Henkel Komm<strong>and</strong>itgesellschaft auf Aktien (Duesseldorf,<br />
DE), April 15 2003.<br />
15. B. C. Arkles. Silacrown ethers, method of making same, <strong>and</strong> use as phasetransfer<br />
catalysts. US Patent 4 362 884, assigned to Petrarch Systems, Inc.<br />
(Levittown, PA), December 7 1982.<br />
16. J.-C. Liu. Instant adhesive composition <strong>and</strong> bonding method employing<br />
same. US Patent 4 906 317, assigned to Loctite Corporation (Newington,<br />
CT), March 6 1990.<br />
17. I. Haiduc. Silicone grease: A serendipitous reagent for the synthesis of exotic<br />
molecular <strong>and</strong> supramolecular compounds. Organometallics, 23(1):3–8,<br />
2004.<br />
18. G. Oddon <strong>and</strong> M. W. Hosseini. Silacrown ethers: Synthesis of macrocyclic<br />
diphenylpolyethyleneglycol mono- <strong>and</strong> disilanes. Tetrahedron Lett., 34(46):<br />
7413–7416, November 1993.<br />
19. J. M. Rooney, D. P. Melody, J. Woods, S. J. Harris, <strong>and</strong> M. A. McKervey.<br />
Instant adhesive composition utilizing calixarene accelerators. EP Patent<br />
0 151 527, assigned to Loctite Irel<strong>and</strong> Ltd, August 14 1985.<br />
20. S. J. Harris. Calixarene derivatives <strong>and</strong> use as accelerators in adhesive compositions.<br />
US Patent 4 866 198, assigned to Loctite Corporation (Newington,<br />
CT), September 12 1989.<br />
21. S. J. Harris, M. A. McKervey, D. P. Melody, J. Woods, <strong>and</strong> J. M. Rooney.<br />
Instant adhesive composition utilizing calixarene accelerators. US Patent<br />
4 636 539, assigned to Loctite (Irel<strong>and</strong>) Limited (Dublin, IE), January 13<br />
1987.<br />
22. S. Attarwala <strong>and</strong> P. T. Klemarczyk. Cyanoacrylate adhesives with improved<br />
cured thermal properties. US Patent 5 328 944, assigned to Loctite Corporation<br />
(Hartford, CT), July 12 1994.<br />
23. R. Lier, R. Vogel, <strong>and</strong> H.-J. Heine. Stabilising cyanoacrylate ester(s) - by<br />
adding acid, e.g. p-toluenesulphonic or citric acid etc., to moulded plastics<br />
used in prodn., storage or use of ester(s). DE Patent 4 109 105, assigned to<br />
Henkel KGAA, September 24 1992.
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24. H.-R. Misiak <strong>and</strong> D. Behn. Stabilized cyanoacrylate adhesives. US Patent<br />
6 642 337, assigned to Henkel Komm<strong>and</strong>itgesellschaft auf Aktien (Duesseldorf,<br />
DE), November 4 2003.<br />
25. P. F. McDonnell. Primer composition <strong>and</strong> use thereof in bonding non-polar<br />
substrates. EP Patent 0 295 013, assigned to Loctite Irel<strong>and</strong> Ltd, December<br />
14 1988.<br />
26. P. F. McDonnell <strong>and</strong> B. J. Kneafsey. Diazabicyclo <strong>and</strong> triazabicyclo primer<br />
compositions <strong>and</strong> use thereof in bonding non-polar substrates. EP Patent<br />
0 295 930, assigned to Loctite Irel<strong>and</strong> Ltd, December 21 1988.<br />
27. P. F. McDonnell <strong>and</strong> B. J. Kneafsey. Diazabicyclo <strong>and</strong> triazabicyclo primer<br />
compositions <strong>and</strong> use thereof in bonding non-polar substrates. US Patent<br />
4 869 772, assigned to Loctite (Irel<strong>and</strong>) Ltd. (Tallaght, IE), September 26<br />
1989.<br />
28. J. C. Liu. Primer for bonding low surface energy plastics with cyanoacrylate<br />
adhesives. EP Patent 0 333 448, assigned to Loctite Corp, September 20<br />
1989.<br />
29. J. C. Liu. Primer for bonding low surface energy plastics with cyanoacrylate<br />
adhesives <strong>and</strong> bonding method employing same. US Patent 5 079 098,<br />
assigned to Loctite Corporation (Hartford, CT), January 7 1992.<br />
30. S. Fukushige et al. Primer for cyanoacrylate adhesive. JP Patent 2 120 378,<br />
assigned to Koatsu Gas Kogyo Co Ltd, May 8 1990.<br />
31. R. Grieves <strong>and</strong> K. G. M. Pratley. Adhesive primer. US Patent 5 837 092,<br />
assigned to Pratley Investments (Proprietary) Limited (ZA), November 17<br />
1998.<br />
32. P. F. McDonnell, G. M. Wren, <strong>and</strong> E. K. Welch, II. Consumer polyolefin<br />
primer. US Patent 5 314 562, assigned to Loctite Corporation (Hartford, CT),<br />
March 24 1994.<br />
33. H. C. Nicolaisen <strong>and</strong> A. Rehling. Primer for cyanoacrylate adhesives <strong>and</strong><br />
use thereof in a bonding method. US Patent 5 133 823, assigned to Henkel<br />
Komm<strong>and</strong>itgesellschaft auf Aktien (Duesseldorf, DE), July 28 1992.<br />
34. A. Hiraiwa, K. Ito, <strong>and</strong> K. Kimura. Primer composition. US Patent 5 292 364,<br />
assigned to Toagosei Chemica Industry Co., Ltd. (Tokyo, JP), March 8 1994.<br />
35. J. G. Woods <strong>and</strong> J. M. J. Frechet. Multi-amine compound primers for bonding<br />
of polyolefins with cyanoacrylate adhesives. US Patent 6 673 192, assigned<br />
to Loctite Corporation (Hartford, CT), January 6 2004.<br />
36. E. Urlaub, J. Popp, V. E. Roman, W. Kiefer, M. Lankers, <strong>and</strong> G. Rossling. Raman<br />
spectroscopic monitoring of the polymerization of cyanacrylate. Chem.<br />
Phys. Lett., 298(1-3):177–182, December 1998.<br />
37. H. R. Misiak. Radiation-curable, cyanoacrylate-containing compositions. US<br />
Patent 6 734 221, assigned to Loctite (R&D) Limited (Dublin, IE), May 11<br />
2004.<br />
38. S. Wojciak <strong>and</strong> S. Attarwala. Radiation-curable, cyanoacrylate-containing<br />
compositions. US Patent 6 726 795, April 27 2004.
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39. K. Kishita <strong>and</strong> N. Ohsawa. Manicure composition for nail. US Patent<br />
6 703 003, assigned to Three Bond Co., Ltd. (Tokyo, JP); Three Bond International<br />
Inc. (West Chester, OH), March 9 2004.<br />
40. S. W. Shalaby. Cyanoacrylate-capped heterochain polymers <strong>and</strong> tissue adhesives<br />
<strong>and</strong> sealants therefrom. US Patent 6 699 940, assigned to Poly Med,<br />
Inc. (Anderson, SC), March 2 2004.<br />
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Patent 6 299 631, assigned to Poly-Med, Inc. (Pendleton, SC), October 9<br />
2001.
14<br />
Benzocyclobutene Resins<br />
Benzocyclobutene (BCB) or bicyclo[4.2.0]octa-1,3,5-triene is also called<br />
cardene, cyclobutabenzene <strong>and</strong> cyclobutarene. Benzocyclobutene was first<br />
synthesized by Finkelstein in 1909 by the 1,4-elimination of bromine from<br />
α,α,α ′ ,α ′ -tetrabromo-o-xylene, 1 as shown in Figure 14.1. Finkelstein’s<br />
thesis was rejected for publication <strong>and</strong> was accidentally discovered more<br />
than 40 years later. 1,5-Hexadiyne trimerizes to give 1,2-bis(benzocyclobutenyl)ethane<br />
(BCBE). Various other methods of synthesis of benzocyclobutene<br />
derivatives have been reported. 2 Suitable monomers are summarized<br />
in Table 14.1.<br />
The four-membered ring in benzocyclobutene (BCB) imparts a ring<br />
strain. Therefore, this class of molecules is especially reactive. Benzocy-<br />
Compound<br />
Table 14.1: Benzocyclobutene Derivatives<br />
Benzocyclobutene (BCB)<br />
Benzocyclobutene-maleimide<br />
1,2-Dihydrocyclobutabenzene-3,6-dicarboxylic acid<br />
2,6-Bis-4-benzocyclobutene benzo[1,2-d:5,4-d ′ ]bisoxazole<br />
Isophthaloyl bis-4-benzocyclobutene<br />
1-Methoxypoly(oxyethylene)benzocyclobutene<br />
3<br />
1-Benzocyclobutenyl vinyl ether<br />
4<br />
2,6-Bis(4-benzocyclobutenyloxy)benzonitrile<br />
5<br />
4-Trimethylsiloxybenzocyclobutene<br />
5<br />
Reference<br />
493
494 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
(a)<br />
CHBr Br<br />
2<br />
NaJ NaJ, H 2<br />
CHBr 2 Br<br />
(b)<br />
O<br />
O<br />
(c)<br />
+<br />
O<br />
O<br />
O<br />
O<br />
(d)<br />
+ +<br />
Figure 14.1: a) Synthesis of Benzocyclobutene, (b) Isomerization, (c) Diels-<br />
Alder Reaction with Maleic anhydride, (d) Cyclotrimerization of 1,5-Hexadiyne
Benzocyclobutene Resins 495<br />
∆<br />
Figure 14.2: Thermal Polymerization of o-Xylylene<br />
clobutene derivatives serve as important building blocks for natural product<br />
syntheses <strong>and</strong> for polymers <strong>and</strong> advanced materials.<br />
In the presence of dienophiles the o-xylylene unit undergoes a Diels-Alder<br />
reaction. However, in the absence of a dienophile the o-xylylene<br />
unit polymerizes as shown in Figure 14.2. The BCB four-membered ring<br />
opens thermally around 200°C to produce o-quinodimethane (QDM), also<br />
known as o-xylylene. 2, 6 o-Xylylene readily undergoes Diels-Alder reactions<br />
with available dienophiles or, in the absence of a dienophile, it reacts<br />
to give a dimer, 1,2,5,6-dibenzocyclooctadiene. The dimerization reaction<br />
is thermodynamically preferred over a Diels-Alder reaction. However, the<br />
Diels-Alder reaction is kinetically favored.<br />
Benzocyclobutene-maleimide monomers (c.f. Figure 14.3) polymerize<br />
to yield exceptionally tough resins with high glass transition temperatures.<br />
Upon heating at above 200°C, the benzocyclobutene ring opens<br />
to form o-xylylene, which then undergoes a cycloaddition or dimerization<br />
reaction. The cyclobutene structure in 1,2-Dihydrocyclobutabenzene-<br />
3,6-dicarboxylic acid can act as a crosslinking site when incorporated in a<br />
polymer.<br />
Poly(benzo[1,2-d4,5-d ′ ]bisthiazole-2,6-diyl)-1,4-phenylene (PBT) is<br />
a rod-like monomer. A thermal crosslinking occurs, when benzocyclobutene<br />
substructures are imbedded in PBT. 7 The mechanism is shown in Figure<br />
14.4.<br />
1-Methoxypoly(oxyethylene)benzocyclobutene has been prepared by<br />
reacting 1-benzocyclobutenyl-1-hydroxyethyl ether with the mesylate of<br />
methoxypoly(oxyethylene). The Diels-Alder reactions of 1-methoxypoly-<br />
(oxyethylene)benzocyclobutene with maleic anhydride <strong>and</strong> N-phenylmaleimide<br />
runs to 100% conversion. 3 1-Benzocyclobutenyl vinyl ether has been<br />
prepared by the elimination of hydrogen bromide from 1-benzocyclobutenyl-1-bromoethyl<br />
ether. This compound was obtained from 1-bromobenzocyclobutene<br />
<strong>and</strong> ethylene glycol. 1-Benzocyclobutenyl vinyl ether can be<br />
polymerized by a cationic mechanism. 4
496 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
C<br />
O<br />
COOH<br />
N<br />
(1)<br />
O<br />
COOH<br />
(2)<br />
O<br />
N<br />
(3)<br />
O<br />
N<br />
O<br />
C<br />
O<br />
C<br />
(4)<br />
Figure 14.3: Benzocyclobutene-maleimide monomer (1),<br />
1,2-Dihydrocyclobutabenzene-3,6-dicarboxylic acid (2)<br />
2,6-Bis-4-benzocyclobutene benzo[1,2-d:5,4-d ′ ]bisoxazole (3),<br />
Isophthaloyl bis-4-benzocyclobutene (4)
Benzocyclobutene Resins 497<br />
ClOC<br />
COCl<br />
+<br />
H 2 N<br />
SH<br />
ClOC<br />
COCl<br />
HS NH 2<br />
Polyphosphoric acid<br />
N<br />
S<br />
S<br />
N<br />
∆<br />
N<br />
S<br />
S<br />
N<br />
Crosslinking<br />
Figure 14.4: Crosslinking of Poly(benzo[1,2-d4,5-d ′ ]bisthiazole-2,6-diyl)-<br />
1,4-phenylene Modified with Benzocyclobutene Structures
498 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
The microwave curing of benzocyclobutene has been described. 8<br />
Microwave curing may speed up the manufacture of parts used in microelectronics.<br />
14.1 MODIFIED POLYMERS<br />
14.1.1 Thermotropic Copolymers<br />
Thermotropic polymers are polymers that are forming liquid crystalline<br />
phases in the melt. Thermotropic copolymers composed of hydroxybenzoic<br />
acid (HBA), hydroxynaphthoic acid (HNA), <strong>and</strong> systematically varying<br />
amounts of hydroquinone (HQ) <strong>and</strong> crosslinkable terephthalic acid have<br />
been described. 9 Also, the chain extension is possible if a BCB functionality<br />
is on one or both ends of a polymer chain. 2<br />
14.1.2 BCB-modified Aromatic Polyamides<br />
The compressive strength of high modulus fibers such as Kevlar can be<br />
improved by the use of a latently crosslinkable monomer, such as 1,2-dihydrocyclobutabenzene-3,6-dicarboxylic<br />
acid. BCB modified aromatic polyamides<br />
as shown in Figure 14.5 can be synthesized by the condensation of<br />
terephthaloyl dichloride <strong>and</strong> 3,5-diaminophenyl-4-benzocyclobutenylketone.<br />
10 The polymers can be crosslinked by the application of heat. These<br />
polymers exhibited broad cure exotherms with onset temperatures in the<br />
range of 238°C, reaching maximum at 275°C. The polymers are useful as<br />
crosslinkable, thermoplastic matrix materials for rigid rod-like composites.<br />
Such composites include composites with poly(p-phenylene benzobisthiazole)<br />
(PBZT), as well as with other benzobisazole polymers. 10<br />
14.1.3 BCB End-capped Polyimides<br />
Benzocyclobutene-terminated polyimide oligomers are useful for high performance<br />
adhesive applications. They are more processable than conventional<br />
polyimide systems, yet form polymers that are thermally stable<br />
at temperatures above 200°C. For example, imide oligomers can be prepared<br />
from 4,4 ′ -[1,3-phenylene(1-methyl ethylidene)]bisaniline (Bis-M),<br />
<strong>and</strong> 4-amino-benzocyclobutene as chain stopper <strong>and</strong> 4,4 ′ -oxydiphthalic anhydride<br />
(ODPA) to arrive at a structure as shown in Figure 14.6. Benzo-
Benzocyclobutene Resins 499<br />
H 2 N<br />
NH 2<br />
O<br />
C<br />
+<br />
Cl<br />
O<br />
C<br />
O<br />
C<br />
Cl<br />
O<br />
O<br />
C<br />
HN<br />
NH<br />
C<br />
O<br />
C<br />
Figure 14.5: BCB-modified Aromatic Polyamides
500 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
H 2 N<br />
O<br />
CH 3 CH 3<br />
C C<br />
NH 2<br />
CH 3 CH 3<br />
Bis-M<br />
O<br />
+<br />
O<br />
O<br />
O<br />
+<br />
H 2 N<br />
O<br />
ODPA<br />
O<br />
4-amino-BCB<br />
Ar<br />
N<br />
O<br />
O<br />
O<br />
N<br />
O<br />
O<br />
Figure 14.6: BCB end-capped Polyimides Prepared from 4,4 ′ -[1,3-Phenylene(1-methyl<br />
ethylidene)]bisaniline (Bis-M), 4-Amino-benzocyclobutene, <strong>and</strong><br />
4,4 ′ -Oxydiphthalic anhydride (ODPA) 11
Benzocyclobutene Resins 501<br />
cyclobutene-terminated polyimides can be cured to form polymers that exhibit<br />
high adhesive strength. 11 The adhesives have been shown to withst<strong>and</strong><br />
exposure to hot wet environment. For example, lap shear samples<br />
immersed in boiling water for three days <strong>and</strong> tested at room temperature<br />
are found to retain over 80% of their strength.<br />
14.1.4 Flame Resistant Formulations<br />
Benzocyclobutene polymers are known as thermosetting polymers having<br />
high thermal stability, but they are flammable. Both the flammability <strong>and</strong><br />
brittleness of BCB resins can be reduced by adding a brominated acrylate,<br />
such as pentabromobenzyl acrylate (PBA) monomer to the BCB resins <strong>and</strong><br />
causing them to react to form a resulting flame retardant thermoset material.<br />
The PBA reduces the brittleness of the cured material by reducing the<br />
crosslinking density. PBA is advantageous because it reacts with the BCB<br />
to create a homogeneous system. 12<br />
14.2 CROSSLINKERS<br />
14.2.1 Modified Poly(ethylene terephthalate)<br />
Thermally crosslinkable polyester copolymers can be synthesized by the<br />
incorporation of a benzocyclobutene-containing terephthalic acid derivative<br />
into poly(ethylene terephthalate) (PET). The cyclobutene moiety on<br />
the chain allows the reactive crosslinking at temperatures at ca. 350°C.<br />
No catalyst is needed <strong>and</strong> no volatile products are formed. Crosslinking<br />
occurs above the melting temperature of 250°C but below the<br />
degradation temperature of 400°C. Therefore, the material can be melt processed.<br />
The degradation temperature <strong>and</strong> the melting temperature decrease<br />
slightly with increased cyclobutene content. The recrystallization <strong>and</strong> glass<br />
transition temperature are insensitive to the cyclobutene content. The limiting<br />
oxygen index (LOI) increases with cyclobutene content. 13<br />
14.3 APPLICATIONS AND USES<br />
Polymer films from BCB formulations exhibit many desirable properties<br />
for microelectronic applications. 14 In particular, they have a low dielectric<br />
constant <strong>and</strong> dissipation factor, low moisture absorption, rapid curing <strong>and</strong>
502 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
E-BCB<br />
DVB-BCB<br />
CH 3 CH 3<br />
Si O Si<br />
CH 3 CH 3<br />
DVS-BCB<br />
Figure 14.7: 1,2-Bis(4-benzocyclobutenyl)ethylene (E-BCB), Bis(benzocyclobutenyl)-m-divinylbenzene<br />
(DVB-BCB), <strong>and</strong> Bis(benzocyclobutenyl)divinyltetramethylsiloxane<br />
(DVS-BCB)<br />
low temperature cure without generating by-products, minimum shrinkage<br />
in curing process, <strong>and</strong> no Cu migration issues. 15<br />
Due to these properties, applications have been found in bumping/<br />
wafer level packaging, optical wave guides, 16, 17 <strong>and</strong> flat panel display.<br />
14.3.1 <strong>Applications</strong> in Microelectronics<br />
Several BCB-containing polymers have been investigated for their use in<br />
coating applications. Suitable monomers are analogues to trans-stilbene,<br />
e.g., 1,2-bis(4-benzocyclobutenyl)ethylene (E-BCB), bis(benzocyclobutenyl)-m-divinylbenzene<br />
(DVB-BCB), <strong>and</strong> bis(benzocyclobutenyl)divinyltetramethylsiloxane<br />
(DVS-BCB).<br />
The structures of the monomers are shown in Figure 14.7.
Benzocyclobutene Resins 503<br />
+<br />
CH 3<br />
Si<br />
CH 3<br />
H 3 C<br />
H 3 C<br />
Si<br />
O<br />
Si<br />
CH 3<br />
CH 3<br />
H 3 C<br />
Si<br />
CH 3<br />
Figure 14.8: Basic Curing Reaction <strong>and</strong> the Structure of the Polymer of DVS-<br />
BCB 2<br />
14.3.1.1 Siloxane-modified Benzocyclobutene<br />
For microelectronics applications, the polymer from DVS-BCB is commonly<br />
used, because it results in a polymer with a high glass transition<br />
temperature of greater than 350°C, a low dielectric constant, a low dissipation<br />
factor, low water absorption, <strong>and</strong> good adhesive properties. 2 The basic<br />
curing reaction <strong>and</strong> the structure of the polymer are shown in Figure 14.8.<br />
With a siloxane bisbenzocyclobutene, high quality spin-on gate dielectric<br />
layers as thin as 50 nm have been fabricated over the semiconductor<br />
layer for polymer field-effect transistors by a solution process. 18 It is<br />
desirable to get materials with low refractive index, <strong>and</strong> thus low dielectric<br />
constant. This can be achieved when the curing reaction is stopped before<br />
vitrification is reached. 19<br />
The treatment with ultraviolet light in the presence of ozone modifies<br />
the chemical properties of BCB, as the polymeric structure of BCB is<br />
degraded <strong>and</strong> becomes soluble in acetone. This behavior may be useful for<br />
BCB reworking after polymerization. 20
504 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
+<br />
Br<br />
OH<br />
O<br />
OH<br />
O<br />
Figure 14.9: Synthesis of BCB-acrylic acid 21<br />
14.3.1.2 Acid Functional Benzocyclobutenes<br />
Acid functional polymers based on benzocyclobutene display excellent<br />
qualities of toughness, adhesion, dielectric constant, <strong>and</strong> low stress. 21 The<br />
synthesis of BCB-acrylic acid is shown in Figure 14.9.<br />
14.3.2 Optical <strong>Applications</strong><br />
Diffractive gratings made from benzocyclobutene can withst<strong>and</strong> temperatures<br />
up to 300°C with only small optical <strong>and</strong> topographical changes after<br />
45 min., whereas conventional photoresist gratings change drastically<br />
within a few minutes under these conditions. 22<br />
The fabrication of Bragg reflector mirrors for GaInAsP/InP lasers<br />
has been described. 23 The process involves multiple sequential steps of<br />
CH 4 /H 2 reactive ion etching (RIE) <strong>and</strong> O 2 plasma etching.<br />
REFERENCES<br />
1. G. Mehta <strong>and</strong> S. Kotha. Recent chemistry of benzocyclobutenes. Tetrahedron,<br />
57(4):625–659, January 2001.<br />
2. M. F. Farona. Benzocyclobutenes in polymer chemistry. Prog. Polym. Sci.,<br />
21(3):505–555, 1996.<br />
3. R. S. Herati. Synthesis of 1-methoxypoly(oxyethylene)benzocyclobutene<br />
<strong>and</strong> its Diels-Alder reactions. J. Polym. Sci. Pol. Chem., 42(8):1934–1938,<br />
April 2004.<br />
4. K. Chino, T. Takata, <strong>and</strong> T. Endo. Synthesis of a poly(vinyl ether) containing<br />
a benzocyclobutene moiety <strong>and</strong> its reaction with dienophiles. J. Polym. Sci.<br />
Pol. Chem., 37(1):59–67, January 1999.<br />
5. L. S. Tan, N. Venkatasubramanian, P. T. Mather, M. D. Houtz, <strong>and</strong> C. L. Benner.<br />
Synthesis <strong>and</strong> thermal properties of thermosetting bis-benzocyclobutene-terminated<br />
arylene ether monomers. J. Polym. Sci. Pol. Chem., 36(14):<br />
2637–2651, October 1998.
Benzocyclobutene Resins 505<br />
6. R. A. Kirchhoff <strong>and</strong> K. J. Bruza. Benzocyclobutenes in polymer synthesis.<br />
Prog. Polym. Sci., 18(1):85–185, 1993.<br />
7. Y.-H. So. Rigid-rod polymers with enhanced lateral interactions. Prog.<br />
Polym. Sci., 25(1):137–157, February 2000.<br />
8. R. V. Tanikella, S. A. B. Allen, <strong>and</strong> P. A. Kohl. Variable-frequency microwave<br />
curing of benzocyclobutene. J. Appl. Polym. Sci., 83(14):3055–3067, April<br />
2002.<br />
9. P. T. Mather, K. P. Chaffee, A. Romo-Uribe, G. E. Spilman, T. Jiang, <strong>and</strong><br />
D. C. Martin. Thermally crosslinkable thermotropic copolyesters: synthesis,<br />
characterization, <strong>and</strong> processing. Polymer, 38(24):6009–6022, November<br />
1997.<br />
10. L.-S. Tan <strong>and</strong> N. Venkatasubramaian. Aromatic polyamides containing keto-benzocyclobutene<br />
pendants. US Patent 5 514 769, assigned to The United<br />
States of America as represented by the Secretary of the Air (Washington,<br />
DC), May 7 1996.<br />
11. E. S. Moyer <strong>and</strong> D. J. D. Moyer. Benzocyclobutene-terminated polymides.<br />
US Patent 5 464 925, assigned to The Dow Chemical Company (Midl<strong>and</strong>,<br />
MI), November 7 1995.<br />
12. M. W. Wagaman <strong>and</strong> T. F. McCarthy. Flame retardant benzocyclobutene<br />
resin with reduced brittleness. US Patent 6 342 572, assigned to Honeywell<br />
International Inc. (Morris Township, NJ), January 29 2002.<br />
13. E. Pingel, L. J. Markoski, G. E. Spilman, B. J. Foran, T. Jiang, <strong>and</strong> D. C.<br />
Martin. Thermally crosslinkable thermoplastic PET-co-XTA copolyesters.<br />
Polymer, 40(1):53–64, January 1999.<br />
14. Y. H. So, P. Garrou, J. H. Im, <strong>and</strong> D. M. Scheck. Benzocyclobutene-based<br />
polymers for microelectronics. Chem. Innov., 31(12):40–47, December 2001.<br />
15. K. Ohba. Overview of photo-definable benzocyclobutene polymer. J. Photopolym.<br />
Sci. Technol., 15(2):177–182, 2002.<br />
16. C. W. Hsu, H. L. Chen, W. C. Chao, <strong>and</strong> W. S. Wang. Characterization<br />
of benzocyclobutene optical waveguides fabricated by electron-beam direct<br />
writing. Microw. Opt. Technol. Lett., 42(3):208–210, August 2004.<br />
17. W. S. Sul, S. D. Kim, S. D. Lee, T. S. Kang, D. An, Y. H. Chun, I. S. Hwang,<br />
J. K. Rhee, <strong>and</strong> K. H. Ryu. Low-characteristic-impedance transmission line<br />
of a benzocyclobutene-based 3-dimensional structure at millimeter-wave frequencies.<br />
J. Korean Phys. Soc., 43(6):1076–1080, December 2003.<br />
18. L. L. Chua, P. K. H. Ho, H. Sirringhaus, <strong>and</strong> R. H. Friend. High-stability<br />
ultrathin spin-on benzocyclobutene gate dielectric for polymer field-effect<br />
transistors. Appl. Phys. Lett., 84(17):3400–3402, April 2004.<br />
19. K. C. Chan, M. Teo, <strong>and</strong> Z. W. Zhong. Characterization of low-k benzocyclobutene<br />
dielectric thin film. Microelectron. Int., 20(3):11–22, 2003.<br />
20. B. Viallet, E. Daran, <strong>and</strong> L. Malaquin. Effects of ultraviolet/ozone treatment<br />
on benzocyclobutene films. J. Vac. Sci. Technol., A, 21(3):766–771,<br />
May–June 2003.
506 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
21. Y. H. So, R. A. DeVries, M. G. Dibbs, R. L. McGee, E. O. Shaffer, II, M. J.<br />
Radler, <strong>and</strong> R. DeCaire. Acid functional polymers based on benzocyclobutene.<br />
US Patent 6 361 926, assigned to The Dow Chemical Company (Midl<strong>and</strong>,<br />
MI), March 26 2002.<br />
22. A. Straat <strong>and</strong> F. Nikolajeff. Study of benzocyclobutene as an optical material<br />
at elevated temperatures. Appl. Optics, 40(29):5147–5152, October 2001.<br />
23. M. M. Raj, J. Wiedmann, S. Toyoshima, Y. Saka, K. Ebihara, <strong>and</strong> S. Arai.<br />
High-reflectivity semiconductor/benzocyclobutene Bragg reflector mirrors<br />
for GaInAsP/InP lasers. Jpn. J. Appl. Phys. Part 1 - Regul. Pap. Short Notes<br />
Rev. Pap., 40(4A):2269–2277, April 2001.
15<br />
<strong>Reactive</strong> Extrusion<br />
<strong>Reactive</strong> extrusion is an attractive route for polymer processing in order to<br />
carry out various reactions including polymerization, grafting, branching,<br />
<strong>and</strong> functionalization. There are monographs on reactive extrusion. 1, 2<br />
In this chapter, we deal mainly with the formation of polymers by<br />
reactive extrusion, i.e., reactive extrusion polymerization. Aspects of reactive<br />
extrusion are covered in other chapters: this includes grafting, compatibilization,<br />
<strong>and</strong> controlled rheology. <strong>Reactive</strong> extrusion polymerization<br />
involves polymerizing a liquid or solid monomer or a prepolymer during<br />
the residence time in the extruder to form a high molecular weight melt.<br />
Low-cost production <strong>and</strong> processing methods for biodegradable<br />
plastics are of great importance, since they enhance the commercial viability<br />
<strong>and</strong> cost-competitiveness of these materials. <strong>Reactive</strong> extrusion is an<br />
attractive route for the polymerization of cyclic ester monomers, without<br />
solvents, to produce high molecular weight biodegradable plastics.<br />
Extruders can be used for bulk polymerization of monomers, like<br />
methyl methacrylate, styrene, lactam, <strong>and</strong> lactide. From a mechanistic<br />
peerspective, nearly all kinds of polymerization have been performed in<br />
an extruder. These include radical polymerization, ionic polymerization,<br />
metathesis polymerization, 3 <strong>and</strong> ring opening polymerization. The techniques<br />
of characterization <strong>and</strong> experimental setup for reactive extrusion<br />
can be found in the literature. 4, 5 The technique is also attractive for melt<br />
spinning. 6, 7<br />
The economics of using an extruder as a bulk polymerization reactor<br />
are favorable when high throughputs <strong>and</strong> control of molecular weight<br />
507
508 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
V<br />
R<br />
H<br />
H<br />
∆T<br />
∆T<br />
Figure 15.1: Balance of an Extruder<br />
are realized. The limitation arises due to the residence time required to<br />
complete the polymerization, which ideally should be less than 5 minutes.<br />
There are significant kinetic, heat transfer, <strong>and</strong> diffusion-related issues<br />
in a bulk polymerization process that make it difficult to develop <strong>and</strong><br />
design processing methods that result in high molecular weight polymer at<br />
high throughputs with a high conversion of the monomer. However, extruders<br />
are ideal process vehicles for this purpose as they can be tailored to<br />
give various flow patterns, residence time distributions <strong>and</strong> shear effects,<br />
each of which affect the polymerization <strong>and</strong> polymer quality.<br />
15.1 EXTRUDER<br />
In this section the reactive extruder depicted in Figure 15.1 is modelled<br />
mathematically. There is an input of monomer on the left side with a volume<br />
rate of ˙V . The average residence time t r is then<br />
t r = , (15.1)<br />
V˙V<br />
when the volume of the extruder is V . The reaction rate in the extruder is Ṙ.<br />
Let us assume for simplicity sake that the rate of reaction is not dependent<br />
on the conversion. The conversion C, as a fraction is then<br />
C = t r Ṙ. (15.2)<br />
To obain full conversion, i.e., C = 1, the residence time should be t r > 1/Ṙ.<br />
The rate of reaction heat generation is calculated by means of Eq. 15.3.<br />
Ḣ = ṘH 0 V (15.3)
Ḣ<br />
H 0<br />
Ṙ<br />
V<br />
Rate of heat released in the whole extruder<br />
Heat released for full conversion in the unit volume<br />
Rate of reaction<br />
Volume of extruder<br />
<strong>Reactive</strong> Extrusion 509<br />
The heat released in the extruder must be conducted through the<br />
walls. Here we neglect that some of the heat is transported away with the<br />
melt. We also neglect that additional heat is generated by friction forces<br />
through kneading. The heat that can be transported though the walls of the<br />
extruder is given by the heat flow equation Eq. 15.4.<br />
Ḣ = kA∆T. (15.4)<br />
Here k is the overall heat transfer coefficient ([Js −1 K −1 m −2 ] (different<br />
from the conductivity coefficient). The area A relates to the volume of<br />
the extruder with a geometry factor g.<br />
V = gA (15.5)<br />
In the case of a cylinder, V = r 2 πh = g2rπh. Let us assume that the heat is<br />
transferred through the envelope of the cylinder. Combining Eq. 15.3 <strong>and</strong><br />
Eq. 15.4, yields Eq. 15.6<br />
∆T = ˙V H 0 g<br />
V k . (15.6)<br />
We have previously implied the condition of full conversion. Eq. 15.6<br />
states that a temperature gradient will be created by the reaction in the<br />
extruder. We are restricted by the temperature difference by the cooling<br />
facilities. For example, the outer temperature is usually not set below the<br />
room temperature for economic reasons. On the other h<strong>and</strong>, the temperature<br />
inside the extruder cannot get too high. Otherwise the material will<br />
pyrolyze. The temperature gradient is limited. Now the temperature difference<br />
will be affected by the throughput. The throughput will be pushed to<br />
a maximum for economic reasons. The heat of reaction for a given process<br />
cannot be changed. However, if there are alternative processes found that<br />
achieve a material with identical properties, the process with a low heat<br />
of conversion should be selected. The geometry factor can be influenced<br />
by the design of the extruder. Clearly, a smaller diameter is advantageous.<br />
This will lead to a design of a longer machine, if a large volume is desired.<br />
The length of a machine is restricted by the mechanical properties of<br />
a screw. The situation is simpler in a chemical plant. There are bent loop<br />
reactors in which the material can freely flow.
510 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
The model described is a very simple, because the temperature gradient<br />
in the melt, the residence time distribution, <strong>and</strong> many other parameters<br />
have not been taken into account. It does provide a basic insight into<br />
important parameters of the device.<br />
More sophisticated models are available in the literature. The reactive<br />
extrusion process in a single-screw extruder has been assessed by<br />
power law fluids undergoing isothermal homogeneous <strong>and</strong> heterogeneous<br />
reactions. The reaction was reported to be first-order. The equation of<br />
conservation of component species was transformed into an eigenvalue<br />
problem. Analytical solutions were developed for the concentration distribution<br />
in the extruder. Expressions for the conversion of the reactant <strong>and</strong><br />
Sherwood number were given. 8<br />
Sometimes severe fluctuations in product quality have been observed.<br />
These fluctuations can be caused by thermal, hydrodynamic, or chemical<br />
instabilities. 9 Some of these instabilities are dependent on the scale of<br />
the equipment. The experimental design is thus important when a reactive<br />
extrusion process is developed in the laboratory for scale up to larger<br />
machines.<br />
15.1.1 Heat of Polymerization<br />
The performance of a reactive extrusion polymerization depends on the<br />
heat of polymerization itself. Table 15.1 summarizes heat <strong>and</strong> entropy of<br />
polymerization for selected compounds.<br />
A review of the data in Table 15.1 reveals that vinyl polymers, such<br />
as propene, styrene, <strong>and</strong> acrylics have a high enthalpy of polymerization.<br />
<strong>Polymers</strong> that are formed by ring opening polymerization have a relatively<br />
lower enthalpy of polymerization. From the point of view of heat transfer<br />
it is desirable to use monomers that have a lower polymerization heat, because<br />
the heat must be removed through the walls of the reactor which has<br />
a limited surface area. Only a low polymerization heat guarantees a high<br />
throughput.<br />
15.1.2 Ceiling Temperature<br />
On the other h<strong>and</strong>, low polymerization heat implies low thermal stability<br />
from the view point of thermodynamics. The free enthalpy of polymerization<br />
is given by Eq. 15.7.
<strong>Reactive</strong> Extrusion 511<br />
Table 15.1: Heats <strong>and</strong> Entropies of Polymerization 10<br />
Compound State a −∆H −∆S Temperature<br />
[kJ/mol] [J/mol/K] [°C]<br />
Propene lc 84 116 25<br />
Acrylic acid lc 67 75<br />
Acrylonitrile lc 77 109 75<br />
Methyl methacrylate lc 56 117 130<br />
Styrene lc 70 149 25<br />
Maleic anhydride ls 59 — 75<br />
1,3-Dioxolan lc 24 76 100<br />
Tetrahydrofuran lc 19 16 25<br />
γ-Butyrolacton lc -5 30 25<br />
Caprolacton lc 17 4 25<br />
D,L-Lactide lc 27 13 127<br />
a lc: from liquid to crystalline<br />
ls: from liquid to solid<br />
∆G<br />
∆H<br />
∆S<br />
Free enthalpy of polymerization<br />
Enthalpy of polymerization<br />
Entropy of polymerization<br />
∆G = ∆H − T ∆S. (15.7)<br />
If ∆G turns negative, then the polymer is no longer stable with respect<br />
to the monomer. Assuming an equilibrium is established, then the<br />
ceiling temperature T c can be calculated by equating Eq. 15.7 to zero.<br />
T c = ∆H<br />
T ∆S<br />
(15.8)<br />
The ceiling temperature yields reasonable results for vinyl monomers,<br />
but in the case of polymers formed by ring opening polymerization,<br />
unreasonable values are obtained.<br />
15.1.3 Strategy of <strong>Reactive</strong> Extrusion<br />
As pointed out above, it is desirable to use materials with a low polymerization<br />
heat in reactive extrusion. Only then can a high throughput be obtained.<br />
On the other h<strong>and</strong>, it is possible to use a mixture of a polymer <strong>and</strong><br />
monomer. The latter is then polymerized in the extruder. This concept can
512 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 15.2: <strong>Polymers</strong> Obtained by <strong>Reactive</strong> Extrusion<br />
Polymer<br />
Radical Polymerization<br />
Reference<br />
Poly(styrene)<br />
11<br />
Poly(butyl methacrylate)<br />
12<br />
Ring opening Polymerization<br />
Poly(lactide)<br />
13<br />
Anionic Polymerization<br />
Poly(styrene)<br />
Styrene-butadiene copolymer<br />
14<br />
Polyamide 12<br />
15<br />
Metathesis Polymerization<br />
Poly(octenylene)<br />
3<br />
reduce the amount of heat to be transferred. In compatibilization, a modified<br />
polymer is used, with only one chemically reactive group in the chain.<br />
In this case the heat of polymerization with respect to volume is reduced<br />
drastically.<br />
On the other h<strong>and</strong>, in injection molding of small articles with a<br />
high surface-to-volume ratio, the viscous melt often must be driven though<br />
small channels, before the melt is placed in the form. In the case of small<br />
articles only small amounts of material are needed. Therefore, the cost of<br />
the material used is less influential in the choice of the process.<br />
The cycle time can be reduced, if the form filling can be reduced.<br />
This can be done by selecting a material that is less viscous. In the case<br />
of small articles, the heat of polymerization is reduced. Therefore, reactive<br />
extrusion is possibly attractive, in the manufacture of small articles.<br />
15.2 COMPOSITIONS OF INDUSTRIAL POLYMERS<br />
Before going into detail, we summarize the polymers that have been obtained<br />
by reactive extrusion according to the mechanism of reaction in Table<br />
15.2.
<strong>Reactive</strong> Extrusion 513<br />
15.2.1 Poly(styrene)<br />
Styrene was polymerized in a twin-screw extruder. The polymerization<br />
reaction mainly occurred in the zone between 400 <strong>and</strong> 1000 mm along<br />
the screw axis in the extruder, corresponding to the residence time of the<br />
reactants ranging from 1 to 4 min in the extruder. Based on dimensionless<br />
analysis, a model of the residence time was established. A kinetic model of<br />
the polymerization was set up under the assumption that the screw extruder<br />
can be treated as an ideal plug flow reactor. 11<br />
A styrene-butadiene multiblock copolymer was synthesized by anionic<br />
polymerization in a twin-screw extruder. The polymerized materials<br />
exhibit a nanometer size styrene <strong>and</strong> butadiene multiblock structure. Further,<br />
they show an ultrahigh elongation at break, which differs considerably<br />
from conventional polymers made by traditional solution polymerizing<br />
methods. 14<br />
Poly(styrene) could be modified by reactive extrusion with trimethylolpropane<br />
triacrylate (TMPTA) <strong>and</strong> dicumyl peroxide (DCP). 16 The<br />
TMPTA increased the molecular weight of PS by a coupling reaction. The<br />
coupling was enhanced in the presence of DCP at a high ratio of TMPTA<br />
to DCP.<br />
15.2.2 Poly(tetramethylene ether) <strong>and</strong> Poly(caprolactam)<br />
A polyetheramide, composed of poly(tetramethylene ether) (PTMEG) as<br />
soft segment <strong>and</strong> poly(caprolactam) as the hard segment, is synthesized in<br />
a one-step, solvent-free process. No volatile by-product is formed during<br />
the process. An isocyanate-terminated telechelic PTMEG was premixed<br />
with caprolactam, <strong>and</strong> this mixture was allowed to react in the twin-screw<br />
extruder to form the polyetheramide triblock copolymer. 17<br />
15.2.3 Polyamide 12<br />
Polyamide 12 was prepared in a reactive extrusion process by the anionic<br />
polymerization of lauryllactam. 15 Sodium hydride was used as initiator<br />
<strong>and</strong> N,N ′ -ethylene-bisstearamide (EBS) was used as activator. The reaction<br />
was complete to 99.5% in less than 2 min at 270°C <strong>and</strong> could be performed<br />
in an internal mixer <strong>and</strong> a twin-screw extruder with co-rotating intermeshing<br />
screws. Rubber-toughened polyamide 12 blends were obtained when<br />
poly(ethylene-co-butyl acrylate) was dissolved in lauryllactam. 1,3-Phen-
514 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
ylene-bis(2-oxazoline) is a suitable chain extender. 18 It reacts with the<br />
terminal carboxyl groups of the polyamide. During the extrusion process,<br />
the residence time distribution (RTD) has been measured by the addition<br />
of ultraviolet <strong>and</strong> ultrasonic detectable tracers.<br />
19, 20<br />
15.2.4 Poly(butyl methacrylate)<br />
Telomers of butyl methacrylate were obtained by reactive extrusion with<br />
1-octadecanethiol as chain transfer agent. The transfer constant to 1-octadecanethiol<br />
was measured. It was shown that the use of relatively high<br />
ratio of chain transfer agent to monomer had no perceptible effect on the<br />
kinetics of telomerization. 12<br />
15.2.5 Poly(carbonate)<br />
Poly(carbonate)s, such as bisphenol A poly(carbonate), are typically prepared<br />
either by interfacial or melt polymerization methods.<br />
The reaction of a bisphenol such as bisphenol A with phosgene in<br />
the presence of water, a solvent such as methylene chloride, an acid acceptor<br />
such as sodium hydroxide, <strong>and</strong> a phase transfer catalyst such as<br />
triethylamine is typical of the interfacial methodology.<br />
The interfacial method for making poly(carbonate) has several inherent<br />
disadvantages. The process requires phosgene which is highly poisonous.<br />
Further, the process requires large amounts of organic solvent.<br />
The reaction of bisphenol A with diphenyl carbonate at high temperature<br />
in the presence of sodium hydroxide as a catalyst is typical for<br />
the melt polymerization method. The melt method, although obviating the<br />
need for phosgene or a solvent, such as methylene chloride, requires high<br />
temperatures <strong>and</strong> relatively long reaction times. As a result, by-products<br />
may be formed at high temperature, such as the products arising by Fries<br />
rearrangement of carbonate units along the growing polymer chains. Fries<br />
rearrangement gives rise to undesired <strong>and</strong> uncontrolled polymer branching<br />
which may negatively impact the polymer’s flow properties <strong>and</strong> performance.<br />
The melt method further requires the use of complex processing<br />
equipment capable of operation at high temperature <strong>and</strong> low pressure, <strong>and</strong><br />
capable of efficient agitation of the highly viscous polymer melt during the<br />
relatively long reaction times required to achieve high molecular weight.<br />
On the other h<strong>and</strong>, poly(carbonate) can be formed under relatively<br />
mild conditions by reacting a bisphenol A with a diaryl carbonate formed
<strong>Reactive</strong> Extrusion 515<br />
O C R<br />
HO<br />
C<br />
R<br />
O<br />
O<br />
Figure 15.2: Fries Rearrangement<br />
by the reaction of phosgene with methyl salicylate. Early procedures used<br />
relatively high levels of transesterification catalysts such as lithium stearate<br />
in order to achieve the desired high molecular weight poly(carbonate).<br />
15.2.5.1 Linear Poly(carbonate)<br />
Poly(carbonate) is prepared by introducing an ester substituted diaryl carbonate,<br />
such as bis(methyl salicyl)carbonate, a bisphenol A, <strong>and</strong> a transesterification<br />
catalyst, e.g., tetrabutylphosphonium acetate (TBPA) into an<br />
extruder. 21 Within the extruder, a molten mixture is formed in which the<br />
reaction between carbonate groups <strong>and</strong> hydroxyl groups occurs, giving rise<br />
to a poly(carbonate) product <strong>and</strong> an ester-substituted phenol by-product.<br />
The extruder may be equipped with vacuum vents which serve to<br />
remove the ester-substituted phenol by-product <strong>and</strong> thus drive the polymerization<br />
reaction toward completion. The molecular weight of the poly-<br />
(carbonate) may be controlled by controlling, among other factors, the feed<br />
rate of the reactants, the type of extruder, the extruder screw design <strong>and</strong><br />
configuration, the residence time in the extruder, the reaction temperature,<br />
the number of vents present in the extruder, <strong>and</strong> the (vacuum) pressure.<br />
The poly(carbonate) reaches a weight-average molecular weight of greater<br />
than 20,000 Dalton.<br />
In a special experimental design, the extruder included 14 segmented<br />
barrels, each barrel having a ratio of length to diameter of about 4, <strong>and</strong> six<br />
vent ports for the removal of the by-product methyl salicylate. Two vents<br />
were configured for the operation at atmospheric pressure <strong>and</strong> four vents<br />
were configured for operation under vacuum. The methyl salicylate formed<br />
as the polymerization reaction took place was collected by means of two<br />
condensers.<br />
The poly(carbonate)s have extremely low levels of Fries rearrangement<br />
products <strong>and</strong> possess a high level of endcapping. Contrary to this is a<br />
bisphenol A poly(carbonate) prepared by a melt reaction method in which<br />
the Fries reaction occurs. The Fries rearrangement is shown in Figure 15.2.
516 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
15.2.5.2 Branched Poly(carbonate)s<br />
Branched poly(carbonate) resins differ from most thermoplastic polymers<br />
used for molding in their melt rheology behavior. Most thermoplastic polymers<br />
exhibit non-Newtonian flow characteristics over essentially all melt<br />
processing conditions. However, in contrast to most thermoplastic polymers,<br />
certain branched poly(carbonate)s prepared from dihydric phenols<br />
exhibit Newtonian flow at normal processing temperatures <strong>and</strong> shear rates<br />
below 300 s −1 .<br />
Copolyester-carbonate resins are prepared analogous to the preparation<br />
of poly(carbonate), but a difunctional carboxylic acid is added. Usually<br />
the carboxylic acid is aromatic <strong>and</strong> used as halide, i.e., isophthaloyl<br />
dichloride <strong>and</strong> terephthaloyl dichloride. Aliphatic diacid components yield<br />
soft segment co-poly(carbonate)s.<br />
Poly(carbonate) <strong>and</strong> copolyester-carbonate resins can be branched<br />
by reaction with tetraphenolic compounds during synthesis. On the other<br />
h<strong>and</strong>, a poly(carbonate) resin possessing a certain degree of branching <strong>and</strong><br />
molecular weight can be produced via reactive extrusion. This is achieved<br />
by melt extruding a linear poly(carbonate) resin with a specific branching<br />
agent <strong>and</strong> an appropriate catalyst system. 22 The resulting molecular weight<br />
increases with branching, but can also decrease if conditions are chosen<br />
that favor degradation.<br />
Branching agents useful to branch linear poly(carbonate)s are polyacrylates<br />
<strong>and</strong> polymethacrylates, in particular pentaerythritol triacrylate<br />
(PETA). Organic peroxides include 2,5-dimethyl-2,5-di(tert-butylperoxy)hexane<br />
(DHBP) <strong>and</strong> 2,5-dimethyl-2,5-di(tert-butylperoxy)-3-hexyne<br />
(DYBP).<br />
Upon melt extrusion, branching <strong>and</strong> crosslinking occurs in the poly-<br />
(carbonate) resin melt. The material is compounded on a melt extruder,<br />
a co-rotating twin-screw extruder under reduced pressure of 0.5 atmospheres,<br />
at a temperature profile of 200 to 300°C.<br />
The assumed mechanism of branching consists of thermal decomposition<br />
of a radical initiator which attacks the methyl groups of the BPA<br />
units in order to create poly(carbonate) macroradicals. The macroradicals<br />
can be recombined by a radical branching agent (compound containing<br />
at least two double bonds) to generate a branched structure. The key to<br />
the process will be the lifetime of the radicals <strong>and</strong> the sensitivity of the<br />
poly(carbonate) backbone versus radicals. A copolyester-poly(carbonate)-<br />
containing long chain aliphatic diacid moieties, such as dodecyl diacid,
Table 15.3: Biodegradable Compositions<br />
Compounds<br />
<strong>Reactive</strong> Extrusion 517<br />
Reference<br />
Poly(lactide)s<br />
23, 23<br />
Poly(ε-caprolactone)<br />
Poly(ε-caprolactone)-grafted starch<br />
24, 25<br />
Poly(propylene) wood flour composites<br />
26<br />
Poly(ε-caprolactone), wood flour or lignin<br />
27<br />
Starch <strong>and</strong> poly(acrylamide)<br />
28<br />
Protein <strong>and</strong> polyester<br />
29<br />
Poly(styrene)-grafted starch<br />
30<br />
is more sensitive to radical attack. Branched poly(carbonate) resins produced<br />
by reactive extrusion are useful blow-moldable resins exhibiting an<br />
enhanced melt strength <strong>and</strong> melt elasticity. The branched poly(carbonate)<br />
products are useful in applications such as 22<br />
• Profile extrusion: of wire <strong>and</strong> cable insulation, extruded bars, pipes,<br />
fiber optic buffer tubes, <strong>and</strong> sheets;<br />
• Blowmolding: of containers <strong>and</strong> cans, gas tanks, automotive exterior<br />
applications such as bumpers, aerodams, spoilers <strong>and</strong> ground<br />
effects packages; <strong>and</strong><br />
• Thermoforming: of automotive exterior applications <strong>and</strong> food packaging.<br />
15.3 BIODEGRADABLE COMPOSITIONS<br />
Many biodegradable compositions have been synthesized <strong>and</strong> investigated.<br />
These are summarized in Table 15.3.<br />
Poly(β-hydroxybutyrate-co-valerate), poly(butylene succinate), poly-<br />
(ethylene succinate) <strong>and</strong> poly(ε-caprolactone) are biodegradable polymers<br />
which are thermally processable. Poly(β-hydroxybutyrate-co-β-hydroxyvalerate)<br />
(PHBV) can be made by both the fermentation process of carbohydrate<br />
<strong>and</strong> an organic acid by a microorganism, e.g., Alcaligenes Eutrophus,<br />
<strong>and</strong> by the use of transgenic plants.<br />
Polyalkylene succinate (PAS) is produced by the reaction between<br />
aliphatic dicarboxylic acids <strong>and</strong> ethylene glycol or butylene glycol. Poly(εcaprolactone)<br />
(PCL) is produced by the ring-opening polymerization of ε-<br />
caprolactone.
518 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
By grafting polar monomers onto poly(β-hydroxybutyrate-co-valerate),<br />
poly(butylene succinate), or poly(ε-caprolactone), the resulting modified<br />
polymer is more compatible with polar polymers <strong>and</strong> other polar substrates.<br />
Useful polar monomers, oligomers, or polymers include ethylenically<br />
unsaturated monomers containing a polar functional group, such<br />
as 2-hydroxyethyl methacrylate (HEMA) <strong>and</strong> poly(ethylene glycol)methacrylate<br />
(PEG-MA).<br />
The grafted biodegradable polymer may contain 1.5 to 20% of<br />
grafted polar monomers. Other reactive ingredients which may be added<br />
to the compositions include free-radical initiators, such as Lupersol 101.<br />
The amount of free-radical initiator ranges from 0.1 to 1.5%. A low<br />
dosage of free-radical initiator cannot initiate the grafting reaction. On the<br />
other h<strong>and</strong>, if the amount of free-radical initiator is too high, it will create<br />
undesirable crosslinking of the polymer composition. Crosslinked polymers<br />
are undesirable, because they cannot be processed into films, fibers<br />
or other products.<br />
The grafting reaction can be performed by a reactive-extrusion process.<br />
31 A particularly useful reaction device is a co-rotating twin-screw<br />
extruder having one or more ports. Such an extruder allows multiple feeding<br />
<strong>and</strong> venting ports <strong>and</strong> provides high intensity distributive <strong>and</strong> dispersive<br />
mixing. The grafting may be achieved in several ways.<br />
1. All of the ingredients, including a biodegradable polymer, a freeradical<br />
initiator, <strong>and</strong> the polar monomer are added simultaneously<br />
to a melt mixing device or an extruder.<br />
2. The biodegradable polymer may be fed to a feeding section of a<br />
twin-screw extruder <strong>and</strong> subsequently melted, <strong>and</strong> a mixture of a<br />
free-radical initiator <strong>and</strong> the polar monomer is injected into the<br />
biodegradable polymer melt under pressure. The resulting melt<br />
mixture is then allowed to react.<br />
3. The biodegradable polymer is fed to the feeding section of a twinscrew<br />
extruder, then the free-radical initiator <strong>and</strong> the polar monomer<br />
are fed separately into the twin-screw extruder at different<br />
points along the length of the extruder. The heated extrusion is<br />
performed under high shear <strong>and</strong> intensive dispersive <strong>and</strong> distributive<br />
mixing resulting in a grafted biodegradable polymer of high<br />
uniformity.<br />
The modified polymer compositions have a greater compatibility
<strong>Reactive</strong> Extrusion 519<br />
with water-soluble polymers, such as polyvinyl alcohol <strong>and</strong> poly(ethylene<br />
oxide), than the unmodified biodegradable polymers.<br />
The compatibility of modified polymer compositions with a polar<br />
material can be controlled by the selection of the monomer, the level of<br />
grafting <strong>and</strong> the blending process conditions. Tailoring the compatibility of<br />
blends with modified polymer compositions leads to better processability<br />
<strong>and</strong> improved physical properties of the resulting blend.<br />
The compositions are biodegradable so that the articles made from<br />
them could be degraded in aeration tanks by aerobic degradation, <strong>and</strong> by<br />
anaerobic degradation in wastewater treatment plants.<br />
PHBV allows only a low cooling rate, such that commercial use of<br />
this material is impractical. On the other h<strong>and</strong>, polylactic acid (PLA) is<br />
brittle. However, a blend of PLA <strong>and</strong> PHBV allows to the PHBV cool<br />
at an acceptable rate <strong>and</strong> also makes PLA more flexible such that these<br />
materials can be used.<br />
15.3.1 Poly(lactide)s<br />
It is generally known that lactide polymers are unstable. The concept of<br />
instability has both advantages <strong>and</strong> disadvantages. The advantage is the<br />
biodegradation or other forms of degradation that occur when lactide polymers<br />
or articles manufactured from lactide polymers are discarded or composted<br />
after completing their useful life. A negative aspect of such instability<br />
is the degradation of lactide polymers during processing at elevated<br />
temperatures as, for example, during melt processing by end user.<br />
Thus, the same properties that make lactide polymers desirable as<br />
replacements for non-degradable petrochemical polymers also create undesirable<br />
effects during production of lactide polymer resins <strong>and</strong> processing<br />
of these resins. In general, poly(lactide) is a relatively brittle polymer<br />
with low impact resistance. Articles made of poly(lactide) may be brittle<br />
<strong>and</strong> prone to shatter under use conditions.<br />
For example, if poly(lactide) is made into articles such as razor holders,<br />
shampoo bottles, <strong>and</strong> plastic caps, these articles may be prone to undesirable<br />
shatter in use. 23 However, compositions with modified physical<br />
properties can avoid these drawbacks.
520 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
H 3 C<br />
O<br />
O<br />
CH 3<br />
O<br />
HO<br />
O<br />
CH<br />
CH 3<br />
C<br />
O<br />
n<br />
Figure 15.3: Ring Opening Polymerization of a Lactide<br />
15.3.1.1 Ring Opening Polymerization of Lactide<br />
The ring opening polymerization of a lactide using an equimolar complex<br />
of 2-ethylhexanoic acid tin(II) salt Sn(Oct) 2 <strong>and</strong> triphenylphosphine PΦ 3<br />
as catalyst exhibits a high reactivity to polymerization that is too high to<br />
allow a continuous single-step reactive extrusion process for bulk polymerization.<br />
The catalyst also delays the occurrence of undesirable backbiting<br />
reactions. The ring opening polymerization is shown in Figure 15.3. A sophisticated<br />
screw design is required to ensure further enhancement of the<br />
polymerization reaction by using mixing elements <strong>and</strong> by the introduction<br />
of shear into the melt. It is possible to design a single stage process using<br />
reactive extrusion to polymerize the lactide into a poly(lactide) that can be<br />
fabricated by most any known polymer processing techniques. 13 Possible<br />
uses of such polymers include food packaging for meat <strong>and</strong> soft drinks,<br />
films for agro-industry, <strong>and</strong> non-wovens in hygienic products. 32<br />
15.3.1.2 Functionalized Poly(lactide)s<br />
A functionalized poly(lactide) is a polymer which has been modified to<br />
contain groups capable of bonding to an elastomer or which have a preferential<br />
solubility in the elastomer. Only a portion of the poly(lactide)<br />
needs to be functionalized in order to gain the benefit of improved impact<br />
strength, however, uniform distribution of the functionalization throughout<br />
the poly(lactide)-based polymer is preferred. The functionalized poly(lactide)<br />
can be created during the lactide polymerization process, for example,<br />
by copolymerizing a compound containing both an epoxide ring <strong>and</strong><br />
an unsaturated bond. The functionalized poly(lactide) polymer, containing<br />
unsaturated bonds, can be blended <strong>and</strong> linked via free radical reactions to<br />
an elastomer which contains unsaturated bonds. The functionalized polymer<br />
can also be prepared subsequent to polymerization reaction, for ex-
<strong>Reactive</strong> Extrusion 521<br />
ample, by grafting a reactive group, such as maleic anhydride (MA), to<br />
the poly(lactide)-based polymer using peroxides. 23 Typically, the resulting<br />
polymer compositions have an impact resistance of at least 0.7 ft − lb/in<br />
(120 kgs −2 ). <strong>and</strong> an impact resistance of at least about 1 ft − lb/in (180<br />
kgs −2 ).<br />
A poly(lactide) can be also functionalized by radical grafting of<br />
maleic anhydride onto it.<br />
33, 34<br />
A concentration of 2% MA in the presence<br />
of 2,5-dimethyl-2,5-di(tert-butylperoxy)hexane suffices to reach up<br />
to 0.7% MA grafted onto the poly(lactide). Increasing the initiator concentration<br />
results in an increase in the grafting of MA, but also in a decrease<br />
in the molecular weight of the polymer. Without initiator, extensive degradation<br />
was observed.<br />
15.3.2 Biodegradable Fibers<br />
One of the most promising biodegradable polymers is poly(lactide) (PLA),<br />
in particular, from the viewpoint of environmental protection. PLA is of<br />
great interest due to its mechanical property profile, its thermoplastic processability,<br />
<strong>and</strong> its biodegradability. Further advantages of PLA compared<br />
to other biodegradable polymers are its renewable origin <strong>and</strong> low price.<br />
PLA is synthesized by the polycondensation of lactic acid or by the<br />
ring-opening polymerization of the lactide. In both cases, lactic acid is the<br />
starting monomer. Lactic acid is commercially produced by means of bacterial<br />
fermentation. Fibers from PLA can obtained in a high-speed melt<br />
spinning <strong>and</strong> spin drawing process. 35 A copolymer of L-lactide <strong>and</strong> 8%<br />
meso-lactide is used that can be obtained by reactive extrusion polymerization.<br />
15.3.3 Poly(ε-caprolactone)<br />
Bulk polymerization of ε-caprolactone in an extruder in the presence of<br />
starch to give a compatibilized blend of poly(ε-caprolactone), starch <strong>and</strong><br />
grafted starch-g-poly(ε-caprolactone) is described in the literature. A suitable<br />
catalyst is aluminum isopropoxide. Aluminum isopropoxide can be<br />
generated in-situ by using tri ethyl aluminum or diisobutyl aluminum hydride.<br />
The lactone should contain less than 100 ppm water <strong>and</strong> should have<br />
an acid value less than 0.5 mgKOH/g. The presence of water <strong>and</strong> free<br />
acid in the reactant mixture is especially significant in the synthesis of high
522 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
molecular weight poly(ε-caprolactone) polymer by reactive extrusion polymerization<br />
since it has a deleterious effect on the kinetics <strong>and</strong> ultimately<br />
leads to lower conversion of monomer to polymer. The impurities interact<br />
with the polymerization catalyst or the propagating species <strong>and</strong> lower<br />
the overall rate of polymerization. In cases where the monomer contains<br />
greater than 100 ppm water, the desired water content may be achieved by<br />
drying it using molecular sieves or calcium hydride (chemical method).<br />
The ring-opening polymerization of ε-caprolactone in the presence<br />
of starch leads to a poly(ε-caprolactone)-grafted starch. The reactant mixture<br />
is extruded at a temperature of 80 to 240°C with residence times up to<br />
12 minutes. 24<br />
15.3.3.1 Blends with Starch<br />
Films produced from poly(ε-caprolactone) <strong>and</strong> its copolymers which have<br />
low melting points, are tacky, as extruded, <strong>and</strong> noisy to the touch <strong>and</strong> have<br />
a low melt strength over 130°C. Due to the low crystallization rate of such<br />
polymers, the crystallization process proceeds for a long time after the production<br />
of the finished articles, followed by an undesirable change of properties<br />
with time.<br />
However, the blending of pre-blended starch with other polymers,<br />
such lactone polymers, improves their processability without impairing the<br />
mechanical properties <strong>and</strong> biodegradability properties. 36 The improvement<br />
is particularly effective with polymers having low melting point temperatures<br />
from 40°C to 100°C.<br />
The pre-blends are obtainable by blending a starch-based component<br />
<strong>and</strong> a synthetic thermoplastic component, such as an ethylene-vinyl<br />
alcohol copolymer in the presence of a plasticizer. Suitable plasticizers are<br />
glycerol, sorbitol, <strong>and</strong> sorbitol monoethoxylate. Urea as additive can destroy<br />
hydrogen bonds of the starch. The addition of urea is advantageous<br />
for the production of blends for film-blowing. By means of extrusion, thermoplastic<br />
blends are obtained wherein the starch-based component <strong>and</strong> the<br />
synthetic thermoplastic component form an interpenetrating structure.<br />
In a first step, starch <strong>and</strong> an ethylene-vinyl alcohol copolymer (1:1)<br />
with minor amounts of plasticizer, <strong>and</strong> other additives such as urea are melt<br />
blended in a twin-screw extruder. This extrudate is pelletized. In a second<br />
step the extrudate from the first step is blended with poly(ε-caprolactone).
<strong>Reactive</strong> Extrusion 523<br />
15.3.3.2 Blends with Wood Flour <strong>and</strong> Lignin<br />
Poly(ε-caprolactone) was compounded in twin-screw extruder together<br />
with wood flour <strong>and</strong> lignin. 27 Maleic anhydride-grafted poly(ε-caprolactone)<br />
(PCL-g-MA) was used as a compatibilizer. The grafting of maleic<br />
anhydride onto PCL was achieved with 2,5-dimethyl-2,5-di(tert-butylperoxy)hexane.<br />
Low contents of grafted maleic anhydride <strong>and</strong> PCL-g-MA<br />
were required to improve both mechanical properties <strong>and</strong> interfacial adhesion.<br />
The addition of lignin retarded the biodegradation.<br />
15.3.4 Cationically Modified Starch<br />
Cationic wheat starch has been prepared by reactive extrusion in a twinscrew<br />
extruder. The modifiers are 2,3-epoxypropyltrimethylammonium<br />
chloride <strong>and</strong> 3-chloro 2-hydroxypropyltrimethylammonium in aqueous<br />
sodium hydroxide (NaOH). 37 A high reaction efficiency can be reached<br />
if a low degree of substitution is adjusted.<br />
15.3.5 Blends of Starch <strong>and</strong> Poly(acrylamide)<br />
Starch-poly(acrylamide) copolymers have been prepared by reactive extrusion<br />
with ammonium persulfate as initiator. The extrusion temperature had<br />
no significant impact on acrylamide conversion. 28<br />
15.3.6 Blends of Protein <strong>and</strong> Polyester<br />
Blends of soy protein <strong>and</strong> biodegradable polyester could be prepared with<br />
glycerol as compatibilizer. 29 Miscibility was only achieved when the soy<br />
protein was processed with glycerol applying high shear at elevated temperatures<br />
in an extruder. There, a partial denaturation of the soy protein<br />
occurred. Extruder screws with large kneading blocks were preferred.<br />
Thermoplastic blends were obtained with high elongation <strong>and</strong> high tensile<br />
strength. When the concentration of protein was increased, a lower degree<br />
of crystallinity <strong>and</strong> a lower melting point was obtained. It is possible to<br />
use a soy protein concentrate instead of a more expensive soy protein with<br />
higher purity.
524 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
15.4 CHAIN EXTENDERS<br />
15.4.1 Recycling of Poly(ethylene-terephthalate)<br />
Chain extenders are low molecular weight compounds that can be used<br />
to increase the molecular weight of polymers. Pyromellitic dianhydride<br />
(PMDA) is a suitable chain extender to increase the molecular weight of<br />
poly(ethylene terephthalate) (PET) industrial scraps with low intrinsic viscosity.<br />
Industrial scraps coming from PET processing plants are in many<br />
cases uncontaminated. However, their viscosity is lowered by the first extrusion.<br />
PMDA has a melting point (283°C) close to that of PET <strong>and</strong> it reacts<br />
within a few minutes under the processing conditions of PET. PMDA is a<br />
tetrafunctional compound, therefore, branching can occur. The PET end<br />
groups consist of carboxyl <strong>and</strong> hydroxyl groups. The chain extension occurs<br />
by a polyaddition between the hydroxyl groups <strong>and</strong> the pyromellitic<br />
dianhydride.<br />
The crucial parameters of the process are the concentration of the<br />
chain extender, the residence time of the polymer in the extruder, <strong>and</strong> the<br />
working temperatures. Dry blends of PET chips <strong>and</strong> PMDA powder were<br />
prepared with different amounts of PMDA (0.25, 0.50, 0.75, <strong>and</strong> 1.00%<br />
by weight). These were vacuum dried for 12 h at 110°C <strong>and</strong> extruded at<br />
280°C. The average residence time is approximately 150 s. An amount<br />
of PMDA from 0.50 to 0.75% is sufficient to result in an increase of M w ,<br />
a broadening of M w /M n , <strong>and</strong> branching phenomena. The recycled polymer<br />
from PET scraps is then suitable for film blowing <strong>and</strong> blow molding<br />
processes. 38<br />
15.4.2 Modified Poly(ethylene terephthalate)<br />
Multifunctional epoxy based modifiers, such as a tetraglycidyl diaminodiphenylmethane<br />
(TGDDM) resin, can be used to increase the melt strength<br />
of PET. The progress conversion with time can be measured by the change<br />
of torque in an internal mixer. With a stoichiometric concentration of<br />
TGDDM, the molecular weight distribution of modified PET shows an<br />
eight-fold increase of the z-average molecular weight (M z ) <strong>and</strong> the presence<br />
of branched molecules of very large mass. 39<br />
Further, a tetrafunctional epoxy based additive can be used to extrude<br />
PET in order to produce PET foams. The molecular structure ana-
<strong>Reactive</strong> Extrusion 525<br />
lysis <strong>and</strong> shear <strong>and</strong> elongation rheological characterization indicates that<br />
branched PET is obtained for small amounts, up to 0.4% of a tetrafunctional<br />
epoxy additive. Gel permeation chromatography (GPC) studies suggest<br />
that a r<strong>and</strong>omly branched structure is obtained, the structure being<br />
independent of the modifier concentration. 40 An increase in the degree of<br />
branching <strong>and</strong> the M w <strong>and</strong> the broadening of the molecular weight distribution<br />
causes an increase in the Newtonian viscosity, the relaxation time,<br />
flow activation energy, <strong>and</strong> the transient extensional viscosity. On the other<br />
h<strong>and</strong>, the shear thinning onset <strong>and</strong> the Hencky strain at the fiber break decrease<br />
markedly.<br />
15.4.3 Poly(butylene terephthalate)<br />
The chain extension reaction in poly(butylene terephthalate) (PBT) can be<br />
achieved by a diglycidyl tetrahydrophthalate with high-reactivity. 41 The<br />
chain extender reacts with the hydroxyl <strong>and</strong> carboxyl end groups of PBT<br />
very fast <strong>and</strong> also at a comparatively high temperature. The chain extension<br />
reaction is complete within 2 to 3 min at temperatures above 250°C. The<br />
chain-extended PBT is thermally more stable than the original polymer.<br />
In order to obtain PBT resins with a high molecular weight, the reactive<br />
extrusion process is simpler <strong>and</strong> cheaper than the post-polycondensation<br />
method.<br />
15.5 RELATED APPLICATIONS<br />
15.5.1 Transesterification<br />
The transesterification is a different concept from polymerization. Transesterification<br />
of mixtures of polyesters <strong>and</strong> oligoesters allows synthesizing<br />
new types of polymers. Block copolyesters have been synthesized from<br />
poly(neopentyl isophthalate) <strong>and</strong> poly(ethylene terephthalate). 42 The esterification<br />
of poly(neopentyl isophthalate) is somehow resistant to transesterification.<br />
Therefore, blocks instead of alternating polyesters will be<br />
obtained. Poly(neopentyl isophthalate) is expected to exhibit high barrier<br />
properties. Therefore, such materials are of interest in the field of beverage<br />
containers.<br />
Similarly, block co-polyesters of PET <strong>and</strong> poly(ε-caprolactone) have<br />
been synthesized by reactive extrusion. In the presence of stannous octoate,<br />
the ring-opening polymerization of ε-caprolactone can be initiated due
526 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
to the hydroxyl end groups of molten PET to form poly(ε-caprolactone)<br />
blocks. 43 A block copolymer with a minimal degree of transesterification<br />
can be obtained under conditions of a fast distributive mixing of the<br />
ε-caprolactone into the high viscous PET.<br />
15.5.2 Hydrolysis <strong>and</strong> Alcoholysis<br />
The continuous hydrolytic depolymerization of a poly(ethylene terephthalate)<br />
was carried out in a twin-screw extruder. The hydrolysis was achieved<br />
by the injection of saturated steam at high pressure. Low molecular weight<br />
products were obtained even at low residence times in the extruder. Therefore,<br />
high depolymerization rates should occur under the conditions selected.<br />
44<br />
α,ω-Diols have been obtained by the alcoholysis of PET through<br />
reactive extrusion. The alcoholysis of PET with diols in the presence of<br />
dibutyltin oxide was carried out in a twin-screw extruder with residence<br />
times of ca. 1 min. Scissions of PET chains are taking place <strong>and</strong> oligoester<br />
α,ω-diols are formed with a number-average of around 1 kDalton. 45 The<br />
study revealed that oligoesters synthesized by reactive extrusion are quite<br />
similar to oligoesters synthesized by batch processes which last many<br />
hours.<br />
15.5.3 Flame Retardant Master Batch<br />
A master batch of an intumescent flame retardant was prepared by reactive<br />
extrusion of melamine phosphate <strong>and</strong> pentaerythritol with a poly(propylene)<br />
carrier in a twin-screw extruder. 46<br />
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16<br />
Compatibilization<br />
There are innumerable binary, ternary, <strong>and</strong> multiple alloys known in metallurgy.<br />
Metals easily form mutual alloys. The situation is completely<br />
different in polymer chemistry, as is pointed out in the literature. 1 Most<br />
of the organic polymers are not mutually miscible. Methods have been<br />
reported for compatibilization of immiscible blends of polymers by reactive<br />
mixing, in which functionalized versions of the polymeric components<br />
react in-situ to form a block copolymer compatibilizer. The fundamental<br />
requirements for a compatibilizer as additive <strong>and</strong> in reactive processing<br />
include the following: 2, 3<br />
• The interfacial tension must be optimized.<br />
• There must be sufficient mixing to achieve the desired fineness of<br />
morphological texture.<br />
• Some of the polymer molecules must contain chemical functional<br />
groups which can react to form primary bonds during the mixing/-<br />
mastication process. The functional groups must be of sufficient<br />
reactivity for reactions to occur across melt phase boundaries.<br />
• The reactions must occur rapidly enough to be completed during<br />
processing in the extruder or mixer within a reasonable time.<br />
• The bonds formed as a result of reactive blending must be stable<br />
enough to survive subsequent processing.<br />
• The adhesion between the phases in the solid state should be enhanced.<br />
• The compatibilization reactions should be fast <strong>and</strong> irreversible.<br />
531
532 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Many new products can be manufactured by melt blending of polymers<br />
to achieve improved properties that are not available in any single<br />
polymeric material, e.g., toughness, chemical resistance, ease of fabrication,<br />
etc.<br />
The use of blends <strong>and</strong> alloys of immiscible polymers has increased<br />
because it is generally less expensive to develop a new blend composition<br />
than to develop new polymers based upon new monomers to meet the need<br />
for specialized polymers.<br />
16.1 EQUIPMENT<br />
Compatibilization reactions are normally performed in an extruder. Also<br />
blenders have been used for discontinuous work. Ultrasonic assisted extrusion<br />
in the molten state has been described in extruders. 4, 5 Ultrasonic<br />
horns placed at the exit of the extruder that are vibrating in the direction<br />
perpendicular to the flow direction introduce longitudinal ultrasonic waves<br />
into the polymer melt. The mechanical performance of polymer blends<br />
subjected was significantly enhanced by ultrasonic treatment in comparison<br />
to the performance of blends not subjected to ultrasonic treatment<br />
with a similar phase morphology.<br />
Ultrasonically assisted melt mixers also have been described. 6 Poly-<br />
(propylene)/poly(styrene)/clay nanocomposites <strong>and</strong> poly(methyl methacrylate)/clay<br />
nanocomposites were prepared by in-situ polymerization<br />
<strong>and</strong> ultrasonic assisted melt mixing.<br />
16.2 BASIC TERMS<br />
16.2.1 Thermodynamic Compatibility<br />
Compatibilizing methods <strong>and</strong> agents are required for such blends, since<br />
most polymers are mutually immiscible <strong>and</strong> have poor interfacial adhesion.<br />
Compatibilizers generally are believed to act at interfaces to improve<br />
interfacial interactions between immiscible polymeric species. It is recognized<br />
that miscibility between polymers is determined by a balance of<br />
enthalpic <strong>and</strong> entropic contributions to the free energy of mixing. While<br />
for small molecules the energy is high enough to ensure miscibility, for<br />
polymers the entropy is almost zero, causing enthalpy to be decisive in determining<br />
miscibility. The change in free energy of mixing (∆G) is written
Compatibilization 533<br />
as<br />
∆G = ∆H − T ∆S (16.1)<br />
where H is enthalpy, S is entropy, <strong>and</strong> T is temperature. For spontaneous<br />
mixing, ∆G must be negative, <strong>and</strong> so<br />
∆H − T ∆S < 0. (16.2)<br />
This implies that exothermic mixtures (∆H < 0) will mix spontaneously,<br />
whereas for endothermic mixtures miscibility will only occur at high temperatures.<br />
2<br />
16.2.2 Thermodynamic Models<br />
Flory’s solution theory was modified by Hamada. 7 This modified theory<br />
was used to predict the miscibility of blends of poly(ethylene oxide) with<br />
poly(methyl methacrylate) (PEO-a-PMMA) <strong>and</strong> with poly(vinyl acetate)<br />
(PEO-PVAc). 8<br />
The interaction parameters of a PEO-a-PMMA blend with the weight<br />
ratio of PEO/aPMMA = 50/50 at the temperature range of 393 to 433 K<br />
<strong>and</strong> PEO-PVAc blends with different compositions <strong>and</strong> temperatures were<br />
calculated from the parameters of the equation of state. The interaction<br />
parameters of the PEO-a-PMMA blend turned out to be negative. The interaction<br />
parameters <strong>and</strong> excess volumes of PEO-PVAc blends are negative<br />
<strong>and</strong> increase with enhancing the content of PEO <strong>and</strong> the temperature.<br />
The miscibility of blends of poly(methyl methacrylate) (PMMA)<br />
<strong>and</strong> poly(ethylene oxide) (PEO) oligomers was studied by temperaturemodulated<br />
DSC. The miscibility domain is larger for the atactic <strong>and</strong> syndiotactic<br />
PMMA than for the isotactic isomer. The Flory-Huggins interaction<br />
parameter χ 1,2 decreases with the increase of the PEO molecular<br />
weight as well as with the syndiotacticity of the PMMA <strong>and</strong> is lower for<br />
the PEO with alkyl modified chain ends. 9<br />
16.2.3 Particle Size<br />
Wu 10 proposed Eq. 16.3 to predict the particle size for polyamide <strong>and</strong><br />
polyester blends containing 15% ethylene/propylene rubber as a dispersed<br />
phase.<br />
d ¯= 4γη±0.84 r<br />
(16.3)<br />
Gη m
534 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
d¯<br />
Average diameter of the droplet<br />
G<br />
Shear rate<br />
γ<br />
Interfacial tension<br />
η r = η d /η m Viscosity ratio<br />
η m Viscosity of the matrix<br />
η d<br />
Viscosity of the dispersed phase<br />
The positive exponent is for η r > 1; the negative exponent is for η r < 1.<br />
16.2.4 Interfacial Slip<br />
The viscosity of uncompatibilized polymer blends often exhibits a negative<br />
deviation from a log-additivity rule at shear rates relevant to processing.<br />
This deviation is attributed to the interfacial slip. The interfacial slip<br />
arises from the loss of entanglements at the interface. The effect of reactive<br />
compatibilization on the interfacial slip has been studied in blends<br />
from ethylene/propylene rubber <strong>and</strong> polyamide 6. It has been demonstrated<br />
that the interfacial slip can be important in uncompatibilized systems<br />
whereas it is suppressed in compatibilized blends. 11<br />
16.2.5 Interpolymer Radical Coupling<br />
By using a solid-state shear pulverization technique in order to blend polymers,<br />
an interpolymer radical coupling reaction has been discovered.<br />
12, 13<br />
This reaction leads to the formation of block copolymers. Pulverization<br />
leads to an intimate mixing, creating a large interfacial area between blend<br />
components, <strong>and</strong> to chain scission reactions, resulting in polymer radicals.<br />
These radicals can cause interpolymer coupling in the solid state. The<br />
interpolymer reaction was proved in a PMMA/PS blend using a pyrenelabelled<br />
PS. The blends were characterized by gel permeation chromatography<br />
with a fluorescence detector. The change in elution times was noted<br />
<strong>and</strong> taken as proof that the interpolymer radical coupling happened at mixing.<br />
16.2.6 Technological Compatibility<br />
However, thermodynamic compatibility need not be attained. Technological<br />
compatibility, where the blend has useful properties, normally is sufficient.<br />
Mechanical or chemical techniques can be used to attain technological<br />
compatibility. Technological compatibility of immiscible polymers<br />
can be produced by
Compatibilization 535<br />
• The addition of a compatibilizer before or during the mixing/blending<br />
process,<br />
• Adjustment of viscosity ratios to favor rapid formation of the desired<br />
phase morphology during mixing,<br />
• In-situ formation of a compatibilizer during the mixing/blending<br />
process, <strong>and</strong><br />
• Introduction of crosslinks in one of the phases.<br />
The objective of technological compatibilization is to produce compositions<br />
which exhibit good ultimate properties, e.g., strength, elongation,<br />
fatigue life, etc. Compatibilized polymer blends exhibit at least some of<br />
the following differences from uncompatibilized polymer blends: reduced<br />
morphological dimensions (smaller domain sizes, thus smaller potential<br />
flaws); improved bonding or adhesion between phases; <strong>and</strong> reduced tendencies<br />
to form highly shaped domains during flow in processing, molding,<br />
etc.<br />
One approach to technological compatibilization is the addition of<br />
a compatibilizer before or during the mixing or blending process, respectively.<br />
Such compatibilizers are frequently a block copolymer. To be efficient,<br />
the compatibilizing block copolymer must possess segments with<br />
chemical structures or solubility parameters, which are similar to or the<br />
same as those of the polymers being blended. A sufficient amount of the<br />
compatibilizing polymer must be located at the interface of the polymer<br />
phases. Usually in this type of compatibilization, one block, A, is chemically<br />
similar to one of the polymer components of the blend <strong>and</strong> the other<br />
block, B, is chemically similar to the other blend component. This method<br />
is usually extremely successful in stabilizing the polymer blend. Nevertheless,<br />
this method is rarely used in commercial applications because of the<br />
high expense usually involved in synthesizing the block copolymer.<br />
Another method of promoting the presence of a compatibilizing block<br />
copolymer at the interfacial region is to use reactive mixing techniques,<br />
whereby the compatibilizing copolymer forms at the interface. In such cases,<br />
polymer molecules of one phase contain functional groups which chemically<br />
interact with molecules of a polymer in an adjacent phase, so that a<br />
compatibilizer could form in the interfacial regions where it is needed.<br />
In other words, reactive compatibilization involves the formation of<br />
a block or graft copolymer via a coupling reaction between the reactive<br />
functional groups of two additives. 2 In Table 16.1 <strong>and</strong> Table 16.2, compatibilizers<br />
for various polymer blends are listed.
536 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Blends<br />
Table 16.1: Compounds for Compatibilization of Polyolefines<br />
Compatibilizer<br />
LDPE/PA6 Diethylsuccinate, 14 glycidyl methacrylate, 15 ethylene <strong>and</strong><br />
acrylic acid copolymer, 16 poly(ethylene) grafted with<br />
maleic anhydride<br />
LDPE/PET Ethylene-propylene copolymer-g-methacryloyl carbamate 17<br />
LDPE/Starch Poly(ethylene-co-glycidyl methacrylate) 18<br />
HDPE/HIPS Styrene/ethylene-butylene/styrene block copolymer 19<br />
HDPE/PA12 Maleic anhydride 20<br />
HDPE/PET Poly(ethylene-co-glycidyl methacrylate)<br />
21, 22<br />
PP/PS Styrene-butadiene triblock copolymer, 23, 24 styrene-ethylene/propylene<br />
diblock copolymer (SEP) 25<br />
PP/PA6 ε-Caprolactam <strong>and</strong> maleic anhydride grafted poly(propylene),<br />
26 isocyanate-modified PP, 27, 28 poly(styrene-b-(ethylene-co-butylene)-b-styrene)<br />
grafted with maleic anhydride<br />
29<br />
EPDM/PTT Grafted ethylene/propylene rubber (EPM-g-MA) 30<br />
Polyolefins Triallyl isocyanurate<br />
Abbreviations<br />
EPDM Ethylene propylene diene rubber<br />
HDPE High density poly(ethylene)<br />
HIPS High impact poly(styrene)<br />
LCP Liquid crystalline polymers<br />
LDPE Low density poly(ethylene)<br />
PA6 Polyamide 6<br />
PA12 Polyamide 12<br />
PE Poly(ethylene)<br />
PET Poly(ethylene terephthalate)<br />
PP Poly(propylene)<br />
PS Poly(styrene)<br />
PTT Poly(trimethylene terephthalate)
Compatibilization 537<br />
Blends<br />
Table 16.2: Compounds for Compatibilization<br />
Compatibilizer<br />
PA6/PPO Styrene/maleic anhydride copolymer,<br />
31, 32<br />
poly(ethylene 1-octene), 33<br />
PA6/PS Styrene/glycidyl methacrylate (SG) copolymers, 34 EPDM<br />
grafted with maleic anhydride, 35 styrene-ethylene-butadiene-styrene<br />
block copolymer grafted with maleic anhydride<br />
35<br />
PA66/PBT Bisphenol A-type epoxy resins 36<br />
PA66/PS Styrene-maleic anhydride copolymer 37<br />
PBT/EVA Maleic anhydride<br />
PBT/EVA/PA6 Maleic anhydride 38<br />
PBT/PEO Poly(ethylene-co-glycidyl methacrylate) 39–41<br />
PC/PVDF Copolymer of methyl methacrylate <strong>and</strong> acrylic acid 42<br />
PE/Fillers Functionalized ethylene copolymers with n-butyl acrylate,<br />
maleic anhydride, epoxy, <strong>and</strong> acrylic acid 43<br />
PE/Wood flour Maleated <strong>and</strong> acrylic acid grafted polyethylenes 44<br />
PET Glycidyl methacrylate grafted rubber 45<br />
PET/LCP Multifunctional epoxies<br />
ABS/PA6<br />
36, 46<br />
poly(methyl methacrylate-co-maleic anhydride)<br />
copolymers 47<br />
PET/PA6 Acrylic modified polyolefin-type ionomer 48<br />
PS<br />
Poly(styrene)-b-poly(ethylene-co-butylene) poly(styrene)<br />
triblock copolymer 49<br />
PS/EPR Interphase modifiers 50<br />
SBR/XNBR Surfactants 51<br />
Abbreviations<br />
Abbreviations<br />
ABS Acrylonitrile-butadiene-styrene PA6 Polyamide 6<br />
EPR Ethylene/propylene rubber PA12 Polyamide 12<br />
EVA Ethylene/vinyl acetate copolymer PA66 Polyamide 6,6<br />
LCP Liquid crystalline polymers PC Poly(carbonate)<br />
PBT Poly(butylene terephthalate) PE Poly(ethylene)<br />
PEO Poly(ethylene-octene) PP Poly(propylene)<br />
PET Poly(ethylene terephthalate) PS Poly(styrene)<br />
PMMA Poly(methyl methacrylate) PVDF Poly(vinylidene<br />
PPO Poly(2,6-dimethyl-1,4- fluoride)<br />
phenylene oxide) SBR Styrene butadiene<br />
XNBR Carboxylated nitrile rubber blend rubber
538 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
16.3 COMPATIBILIZATION BY ADDITIVES<br />
The next topic is compatibilization by additives <strong>and</strong> reactive compatibilization.<br />
This classification is somewhat arbitrary. In fact, additives react<br />
chemically with some ingredients of a blend to increase the compatibility<br />
of their constituents. Section 16.4 discusses reactive compatibilization<br />
issues where the compatibilizer is essentially formed during the blending.<br />
16.3.1 Poly(ethylene) Blended with Inorganic Fillers<br />
Aluminum hydroxide <strong>and</strong> magnesium hydroxide blends with poly(ethylene)<br />
composites can be compatibilized with functionalized polyethylenes.<br />
Suitable compatibilizers are hydroxyl or carboxylic acid functionalized<br />
ethylene copolymers prepared with metallocene catalysts.<br />
Compatibilizer precursors are n-butyl acrylate, maleic anhydride,<br />
epoxy, <strong>and</strong> acrylic acid. 43 These polymeric compatibilizers improve adhesion.<br />
The improved adhesion is reflected in the mechanical properties,<br />
such as stiffness <strong>and</strong> toughness. The flame retardancy imparted by the inorganic<br />
hydroxides does not deteriorate upon addition of compatibilizers.<br />
16.3.2 Filler Materials without Chemical Compatibilizers<br />
Filler materials modify the melt elasticity <strong>and</strong> viscosity of a dispersed<br />
phase of a lower viscosity material sufficiently to result in a reduction of<br />
the efficiency of dispersed phase particle collisions in a higher viscosity<br />
matrix. Since the efficiency of such collisions is inversely related to the<br />
modulus of the dispersed phase, for instance, more elastic, higher modulus<br />
dispersed phase particles have a lower probability of coalescing upon collision.<br />
This reduces the coalescence of the dispersed phase under conditions<br />
of high shear experienced, for example, during injection molding.<br />
Selective precompounding or extrusion of polymer components with<br />
fillers can change the viscosity <strong>and</strong>/or elasticity of the dispersed phase<br />
polymer prior to forming the blend, so that a customized viscosity/elasticity<br />
ratio of the blend components may be achieved, obviating the need<br />
for added compatibilizers. 52<br />
Matrix phase polymers include a wide range of polymers. The volume<br />
of the matrix phase polymer is greater than about 65%. There is a<br />
wide range of suitable materials that may be used as filler material, such<br />
as carbon black, hydrated amorphous silica, fumed silica, fumed titanium
Compatibilization 539<br />
dioxide, fumed aluminum oxide, diatomaceous earth, talc, <strong>and</strong> calcium<br />
carbonate.<br />
In general, blends may be formed by dispersing the filler material<br />
within the dispersed phase polymer to form a modified dispersed phase<br />
polymer, then dispersing the modified material within the matrix phase<br />
polymer.<br />
The first step is a melt blending of the filler with the dispersed phase<br />
polymer. The goal of the first step is to ensure that the filler is completely<br />
wetted by the polymer, <strong>and</strong> to take advantage of the strong interaction of<br />
the dispersed phase polymer <strong>and</strong> the filler surface. If the interactions are<br />
not sufficiently favorable, it may be desirable to pretreat the filler to ensure<br />
strong interactions between the filler <strong>and</strong> the dispersed phase so that the<br />
filler stays confined in the dispersed phase.<br />
The modified dispersed phase polymer is then mixed with the matrix<br />
phase polymer. Typically, this mixing occurs at a temperature which<br />
is less than the melting point of the matrix phase polymeric component.<br />
In the subsequent mixing step the components are well mixed in a melt<br />
mixing process. However, due to the strong interaction between the filler<br />
<strong>and</strong> the dispersed phase polymer, the filler stays substantially confined in<br />
the dispersed phase.<br />
16.3.3 Modified Inorganic Fillers<br />
16.3.3.1 Magnesium Hydroxide<br />
For high molecular weight medium density poly(ethylene) (MDPE) compounds,<br />
the magnesium hydroxide filler can be surface-treated by fatty acid<br />
coatings. The surface treatment modifies the yield stress <strong>and</strong> modulus.<br />
Maxima are observed close to the monolayer coverage of the acid<br />
modifier. Acid-group terminated poly(ethylene) (ATPE) coatings produce<br />
the highest yield stress, as a result of physical interaction with the matrix<br />
polymer. The thermomechanical history during processing also modifies<br />
physical properties of MDPE/Mg(OH)(2) composites to some extent.<br />
Anisotropic effects include molecular orientation <strong>and</strong> filler particle<br />
alignment induced by shear stress during the injection molding process.<br />
The use of organo-acid coatings reduces polymer-particle surface interaction<br />
<strong>and</strong> thermodynamic work of adhesion, leading to an improved dispersion<br />
<strong>and</strong> enhanced mechanical properties.
540 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
16.3.3.2 Fumed Silica<br />
The compatibility of PP/PS blends can be improved by the addition of<br />
nano-silica particles. Fumed SiO 2 particles with a size of 10 to 30 nm<br />
are treated with octamethylcyclotetraoxysilane. 53 Possible explanations<br />
for the compatibilization effect caused by the nano-silica particles have<br />
been pointed out:<br />
1. The enhanced compatibility is caused by the adsorption of both PP<br />
<strong>and</strong> PS molecules onto the surface of the silica.<br />
2. By the introduction of the particles, the viscosity changes. This<br />
causes a retardation of the coalescence of the dispersed PS particles.<br />
It seems that the compatibilization in PP/PS blends by fumed silica<br />
particles is controlled by the kinetics rather than by thermodynamics.<br />
16.3.4 Clay Nanocomposites<br />
Maleic anhydride grafted poly(ethylene) (maleated poly(ethylene))/ clay<br />
nanocomposites can be prepared by simple melt compounding. The exfoliation<br />
<strong>and</strong> intercalation behaviors depend on the hydrophilicity of poly-<br />
(ethylene) grafted with maleic anhydride <strong>and</strong> the chain length of organic<br />
modifier in the clay. When the number of methylene groups in the alkylamine<br />
acting as organic modifier is more than 16, an exfoliated nanocomposite<br />
is formed. Unmodified LLDPE shows only an intercalation, which does<br />
not depend on the initial spacing between clay layers. 54 In a similar study<br />
another group used octadecylamine-modified montmorillonite clay. 55<br />
16.3.5 Thermoplastic Elastomers<br />
Thermoplastic elastomers with 50% poly(ethylene terephthalate) (PET),<br />
30% compatibilizer, i.e., glycidyl methacrylate grafted rubber or glycidyl<br />
methacrylate-containing copolymer <strong>and</strong> 20% other rubbers, can be produced<br />
by melt blending with <strong>and</strong> without dicumyl peroxide initiated curing.<br />
The compatibility of the blend with PET is strongly improved when a<br />
nitrile rubber (NBR) with a high content of acrylonitrile <strong>and</strong> an ethylene/-<br />
glycidylmethacrylate copolymer (EGMA) or an ethylene/propylene rubber<br />
grafted with GMA (EPR-g-GMA), are used as rubber <strong>and</strong> compatibilizer<br />
respectively. 45
Compatibilization 541<br />
The reactive compatibilization of poly(butylene terephthalate) (PBT)<br />
with an epoxide-containing rubber is influenced by the concentration of the<br />
reactive groups. The interfacial reaction is slow <strong>and</strong> not controlled by diffusion.<br />
The kinetics of the interfacial grafting only depends on the concentration<br />
of the reactive functions in the vicinity of the interface. The final<br />
particle size correlates to the amount of copolymer formed in-situ at the<br />
blend interface. 56<br />
<strong>Reactive</strong> compatibilization of a poly(butylene terephthalate) (PBT)<br />
<strong>and</strong> ethylene/vinyl acetate copolymer (EVA) can be achieved by maleic<br />
anhydride (MA).<br />
The graft copolymerization of EVA with MA is done, using dicumyl<br />
peroxide (DCP) as an initiator, by melt-free radical grafting. PBT is then<br />
blended with the EVA-g-MA obtained in the first step. The impact strength<br />
of PBT/EVA-g-MA (80/20) blend showed about threefold increase in comparison<br />
with a comparable PBT/EVA blend without compatibilizer. 57<br />
16.3.6 Polyamide 6,6 <strong>and</strong> Poly(butylene terephthalate)<br />
A bisphenol A-type solid epoxy resin is a low cost <strong>and</strong> efficient compatibilizer<br />
for immiscible <strong>and</strong> incompatible blends of polyamide 6,6 (PA66)<br />
<strong>and</strong> poly(butylene terephthalate) (PBT). 36 The epoxy resin is able to form<br />
in-situ a PBT-co-Epoxy-co-PA66 mixed copolymer at the interface. This<br />
mixed copolymer with both segments structurally identical to both base<br />
polymers will anchor along the interface, <strong>and</strong> functions as an effective<br />
compatibilizer for the PA66/PBT blends.<br />
16.3.7 Poly(ethylene)/Wood Flour Composites<br />
Functionalized polyolefins such as maleated <strong>and</strong> acrylic acid grafted polyethylenes,<br />
maleated poly(propylene) (PP-g-MA), <strong>and</strong> styrene-ethylene/-<br />
butylene-styrene triblock copolymer (SEBS-g-MA) have been tested to reduce<br />
the interfacial tension between a poly(ethylene) matrix <strong>and</strong> the wood<br />
filler.<br />
Among these compounds, maleated linear low density poly(ethylene)<br />
shows a maximum tensile <strong>and</strong> impact strength of the composites. This<br />
is effected by the improved compatibility with the HDPE matrix. 44
542 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
16.3.8 Recycled Polyolefins<br />
Post-consumer high density poly(ethylene) (HDPE) has been investigated<br />
for use in recycling in large-scale injection moldings. Blends with recycled<br />
high density poly(ethylene) (re-HDPE) <strong>and</strong> low density poly(ethylene)<br />
(LDPE) or linear low density poly(ethylene) (LLDPE) are considered<br />
to improve the mechanical properties. 58<br />
The mechanical <strong>and</strong> rheological data show that LDPE is a better<br />
modifier for re-HDPE than LLDPE. The mechanical properties of re-HD-<br />
PE/LLDPE blends are lower than the additive properties, i.e. they exhibit<br />
a negative synergism. This demonstrates the lack of compatibility between<br />
the blend components in the solid state. The mechanical properties of<br />
blends of recycled HDPE <strong>and</strong> LDPE are equal to or higher than calculated<br />
from linear additivity.<br />
16.3.9 Block Copolymers<br />
Poly(styrene) (s-PS)/ethylene/propylene rubber (EPR) blends have been<br />
compatibilized with triblock copolymers such as poly(styrene)-b-poly(ethylene-co-butylene)<br />
poly(styrene) (SEBS). 49 The size of the dispersed EPR<br />
phase in s-PS/EPR/SEBS blends decreases <strong>and</strong> the particle size distribution<br />
becomes narrower with increasing amounts of SEBS in the blends. Low<br />
molecular weight SEBS is more effective in increasing the impact strength<br />
of s-PS/EPR blend than a high molecular weight SEBS. This correlates<br />
with the fact that s-PS/EPR blends compatibilized by the low molecular<br />
weight SEBS have good adhesion between the s-PS matrix <strong>and</strong> dispersed<br />
EPR particles, whereas the s-PS/EPR blends compatibilized by the high<br />
molecular weight SEBS exhibit poor adhesion between phases. It is suggested<br />
that the blocks in the low molecular weight SEBS penetrate into<br />
the corresponding phase more easily than the blocks in the high molecular<br />
weight SEBS.<br />
The functionalization of a styrene-b-(ethylene-co-1-butene)-b-styrene<br />
triblock copolymer (SEBS) <strong>and</strong> styrene-co-butadiene (SBR) r<strong>and</strong>om<br />
copolymer takes place in the melt with diethyl maleate (DEM) <strong>and</strong> dicumyl<br />
peroxide (DCP) as initiator. Under these conditions, the functionalization<br />
proceeds with a large preference at the aliphatic carbons of the polyolefin<br />
block. 59 The situation is similar, when maleic anhydride is used. 60<br />
Triblock copolymers of poly[styrene-b-(ethylene-co-butylene)-b-styrene]<br />
(SEBS) or poly(styrene-b-(ethylene-co-butylene)) (SEB) can be used
Compatibilization 543<br />
to compatibilize high density poly(ethylene) <strong>and</strong> syndiotactic poly(styrene)<br />
blends. The phase size of the dispersed s-PS particles is significantly reduced<br />
by the addition of all these copolymers, <strong>and</strong> the interfacial adhesion<br />
between the two phases is dramatically enhanced. The mechanical performance<br />
of the modified blends is dependent not only on the interfacial<br />
activity of the copolymers but also on the mechanical properties of the copolymers,<br />
in particular at a high copolymer concentration. The addition of<br />
compatibilizers to HDPE/s-PS blends results in a significant reduction in<br />
crystallinity of both HDPE <strong>and</strong> s-PS. The Vicat temperature of the blends<br />
indicates an improved heat resistance of the HDPE by addition of incorporation<br />
of 20% s-PS. 61<br />
The lack of adequate characterization techniques has been a hindrance<br />
to the effective exploitation <strong>and</strong> study of co-continuous morphologies<br />
in polymer blends. Blends of high density poly(ethylene) <strong>and</strong> poly-<br />
(styrene) blends have been compatibilized with a triblock copolymer interfacial<br />
modifier. The influence of the triblock copolymer interfacial modifier,<br />
hydrogenated styrene-ethylene-butadiene-styrene, has been investigated<br />
by the measurement of the surface area <strong>and</strong> the pore dimensions of<br />
the blends after solvent extraction of one of the phases. The Brunauer Emmett<br />
Teller (BET) nitrogen adsorption technique <strong>and</strong> mercury porosimetry,<br />
respectively, have been used. Mercury porosimetry can lead to erroneous<br />
information, while the BET method appears to be both rapid <strong>and</strong> consistent<br />
with SEM observation. The specific surface area of the compatibilized<br />
co-continuous blend system is five-fold higher than that of its non-compatibilized<br />
counterpart, while the pore diameter of the extracted compatibilized<br />
blend is reduced five-fold. Using the BET technique, it is possible to generate<br />
an emulsification curve in the continuous region, demonstrating the<br />
efficiency of the interfacial modifier. 62<br />
The Brunauer Emmett Teller equation 63 can be used to determine the<br />
surface area of solids. It takes into account a multiple layer absorption, in<br />
contrast to the earlier derived Langmuir adsorption isotherm. The volume<br />
of gas absorbed at the surface V is related to the pressure p applied by Eq.<br />
16.4.<br />
p<br />
V(p − p 0 ) = 1<br />
V m C + C − 1<br />
V m C<br />
p<br />
p 0<br />
(16.4)<br />
V m<br />
p 0<br />
C<br />
Volume of a monomolecular layer<br />
Saturation pressure<br />
Constant related to activation energy of absorption <strong>and</strong> desorption
544 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
16.3.10 Impact Modification of Waste PET<br />
The impact properties of waste poly(ethylene terephthalate) can be improved<br />
by melt blending with a polyolefinic elastomer, in a co-rotating<br />
twin-screw extruder. The compositions have an elastomer content up to<br />
10%. Poly(ethylene-co-acrylic acid) is a suitable compatibilizer for this<br />
system. 64 The incorporation of polyolefinic elastomer improves the impact<br />
properties of PET significantly.<br />
16.3.11 Starch<br />
Starch is a carbohydrate that is produced by many plants to store chemical<br />
energy. It is a polymer built from glucose. The main components are amylose<br />
which is a linear polymer <strong>and</strong> amylopectin which is branched.The ratio<br />
of amylose to amylopectin varies with origin. Most common are potato<br />
starch, maize starch, soybean starch, <strong>and</strong> rice starch.<br />
Sago is manufactured from the tree trunks of an Indian pomp tree.<br />
In grain form it is exported to Europe <strong>and</strong> America where it is used in the<br />
food industries. 65<br />
Cassava is also known as manioc, manihot, yucca, m<strong>and</strong>ioca, sweet<br />
potato tree, <strong>and</strong> tapioca. It originates from tropical regions of America <strong>and</strong><br />
is now cultivated in Africa <strong>and</strong> East Asia. It has a particular high starch<br />
content. The starch is collected from its tuberous roots. Tapioca starch is<br />
an important carbohydrate in tropical countries. When gelatinized it results<br />
in a highly cohesive paste.<br />
16.3.11.1 Sago Starch<br />
Sago starch is a possible filler for polyolefins. Sago starch can be chemically<br />
modified through esterification using 2-dodecen-1-yl succinic anhydride<br />
<strong>and</strong> propionic anhydride in solvents, such as N,N-dimethylformamide,<br />
triethylamine, or toluene. Evidence of anhydride modification was<br />
indicated by a weight gain of the material <strong>and</strong> was further confirmed by<br />
infrared spectroscopy. Starch modified with 2-dodecen-1-yl succinic anhydride<br />
<strong>and</strong> propionic anhydride can be used for the preparation of composites.<br />
66 In unmodified blends of starch <strong>and</strong> LLDPE, the tensile modulus<br />
<strong>and</strong> water absorption increase with increasing starch content.<br />
However, the tensile strength <strong>and</strong> the elongation at break show a<br />
decrease with increasing starch content. Modified starch shows improved
Compatibilization 545<br />
mechanical properties <strong>and</strong> water absorption properties in comparison to<br />
unmodified starch.<br />
16.3.11.2 Cassava <strong>and</strong> Tapioca Starch<br />
Cassava starch can be chemically modified by radiation induced grafting<br />
with acrylic acid to obtain a cassava starch graft poly(acrylic acid). This<br />
product is further modified by esterification <strong>and</strong> etherification with poly-<br />
(ethylene glycol) <strong>and</strong> propylene oxide, respectively. The chemical modifications<br />
of cassava starch cause it to become partially hydrophobic. It can<br />
be used for blending with LDPE. 67<br />
A functionalized epoxy resin, poly(ethylene-co-glycidyl methacrylate),<br />
can be used as a compatibilizer for blends of low density poly(ethylene)<br />
(LDPE) <strong>and</strong> tapioca starch. The mechanical properties are significantly<br />
improved by the addition of the epoxy compatibilizer, approaching<br />
values close to those of virgin LDPE. Scanning electron micrographs of<br />
the compatibilized blends show a ductile failure structure, which obviously<br />
contributes to the enhanced mechanical properties. 18<br />
16.3.12 Blends of Cellulose <strong>and</strong> Chitosan<br />
Blends of the naturally occurring polysaccharides, cellulose <strong>and</strong> chitosan,<br />
can be obtained in the solid phase by the combined action of high pressure<br />
<strong>and</strong> shear deformation. A diepoxide can act as a crosslinking agent,<br />
even when cellulose reacts with chitosan without the compatibilizer. The<br />
crosslinking agent reacts predominantly at the amino groups of chitosan,<br />
forming a three-dimensional network. The cellulose macromolecules are<br />
located within <strong>and</strong> partially bound with this network by the crosslinks. The<br />
formation of the network results in the insolubility of cellulose-chitosan<br />
compositions in acidic <strong>and</strong> alkaline aqueous media. 68<br />
16.4 REACTIVE COMPATIBILIZATION<br />
It is a common practice to blend existing polymers to obtain new materials,<br />
instead of searching for new monomers, which is often more costly <strong>and</strong><br />
time-consuming.<br />
Addition of block copolymers or the use of functionalized homopolymers<br />
which can react to form copolymers in-situ is an effective method
546 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
CH 3<br />
C CH 2<br />
CH 3<br />
C<br />
NCO<br />
H 3 C<br />
TMI<br />
Figure 16.1: 3-Isopropenyl-α,α-dimethylbenzene isocyanate (TMI)<br />
for compatibilization of two immiscible phases in a polymer blend <strong>and</strong> prevention<br />
of coalescence.<br />
The role of compatibilization is to stabilize the morphology <strong>and</strong><br />
modify the interfacial properties of the blend. This is achieved by adding<br />
or creating in-situ, during the blending process, a third component, often<br />
called an interfacial agent, emulsifier or compatibilizer. 69<br />
<strong>Reactive</strong> compatibilization allows generating the compatibilizer insitu<br />
at the interfaces directly during blending. The presence of a copolymer<br />
also accelerates the melting of polymer blends.<br />
70, 71<br />
In the case of poly(propylene)/polyamide 6 (PA6), a graft copolymer<br />
can be formed easily during blending, if a fraction of the poly(propylene)<br />
chains are functionalized with a functional vinyl monomer such as maleic<br />
anhydride. The anhydride then reacts with the terminal amine groups of<br />
polyamide 6. Since the compatibilizer is formed in-situ at the interfaces,<br />
placing it at the interfaces is straightforward.<br />
In general, the functional groups must be stable enough under<br />
the process conditions, to withst<strong>and</strong> high temperature <strong>and</strong> exposure<br />
to air <strong>and</strong> humidity. Poly(propylene) can also be functionalized<br />
with 3-isopropenyl-α,α-dimethylbenzene isocyanate, 69, 72 c.f. Figure<br />
16.1. 2,5-Dimethyl-2,5-di(tert-butylperoxy)hexane (DHBP) is a suitable<br />
free-radical initiator for the functionalization of poly(propylene) with<br />
3-isopropenyl-α,α-dimethylbenzene isocyanate (TMI). The free radical<br />
grafting is performed at 200°C.<br />
In the second step, an in-situ polymerization of ε-caprolactam in the<br />
presence of poly(propylene) <strong>and</strong> an in-situ compatibilization of the functional<br />
poly(propylene) with the PA6 occurs. Activator <strong>and</strong> catalyst for the
Compatibilization 547<br />
polymerization of ε-caprolactam are sodium chloride <strong>and</strong> ε-caprolactam<br />
blocked hexamethylene diisocyanate.<br />
The compatibilizing efficiency is very high compared with that of the<br />
classical compatibilization method starting with a premade PP, PA6 <strong>and</strong> a<br />
maleic anhydride modified PP. In the classical compatibilization method,<br />
a copolymer of PP <strong>and</strong> PA6 is formed by an interfacial reaction between<br />
maleic anhydride functionalized PP <strong>and</strong> the terminal amine group of PA6.<br />
Thus, the amount of copolymer formation depends very much on the interfacial<br />
volume available in the system. This is usually very small for<br />
immiscible polymer pairs. On the other h<strong>and</strong>, when one polymer component<br />
is formed in-situ, the amount of the copolymer formation is no longer<br />
limited by the interfacial. 69<br />
Another type of reactive compatibilizer is 4,4 ′ -diphenylmethane<br />
carbodiimide (OCDI), 4,4 ′ -diphenylmethane bismaleimide (BMI), <strong>and</strong><br />
2,2 ′ -(1,4-phenylene)bisoxazoline (BOX). OCDI <strong>and</strong> BOX are chain extenders<br />
<strong>and</strong> react with the carbonyl groups of PA6. On the other h<strong>and</strong>, BMI<br />
has a lower reactivity. Grafting of BMI to PP chains improves the compatibility<br />
in a PA6/PP blend <strong>and</strong> increases PP adhesion to glass fiber. 73<br />
The functionalization of a propylene moiety with a bismaleimide is<br />
shown in Figure 16.2. Among acrylic acid (AA), bismaleimide (BMI) <strong>and</strong><br />
maleic anhydride as compatibilizing agent for an isotactic poly(propylene)<br />
(IPP)/polyamide 6 blend, the effectiveness increases in the following order:<br />
IPP-AA < IPP-BMI
548 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
O<br />
N<br />
CH 2<br />
N<br />
O<br />
O<br />
CH CH 3<br />
CH 2<br />
+<br />
CH CH 3<br />
CH 2<br />
O<br />
O<br />
O<br />
N<br />
CH 2<br />
N<br />
O<br />
C CH 3<br />
CH 2<br />
CH CH 3<br />
H<br />
CH 2<br />
Figure 16.2: Functionalization of a Propylene Moiety with a Bismaleimide 78<br />
of BMI. A possible mechanism of compatibilization has been proposed.<br />
The shear forces during melt mixing cause the rupture of chemical bonds<br />
in the polymers, which form macroradicals of PET, LDPE, or EPDM.<br />
Subsequently, the macroradicals react with BMI to form copolymers<br />
of the respective constituents. These copolymers act as compatibilizers. 79<br />
16.4.1 Coupling Agents for Compatibilization<br />
Coupling agents can be used to form chemical bonds between a polyolefin<br />
<strong>and</strong> a second polymer. Blends of polyolefins <strong>and</strong> other polymers can be<br />
coupled by a peroxide, such as dicumyl peroxide <strong>and</strong> triallyl isocyanurate<br />
as coupling agent. A hexafunctional coupling agent for polyolefins is<br />
hexa(allylamino)cyclotriphosphonitrile (HAP). 80<br />
For the coupling of polyamides, triallyl isocyanurate, maleic anhydride<br />
<strong>and</strong> undecenal have been described.
Compatibilization 549<br />
16.4.1.1 Diamines<br />
Diamines are suitable to couple poly(acrylic acid-co-ethylene) <strong>and</strong> poly-<br />
(maleic anhydride-co-styrene). 81 Melt blends of maleic anhydride grafted<br />
poly(styrene) with amino-methacrylate-grafted poly(ethylene) display a<br />
somewhat finer morphology <strong>and</strong> improved mechanical properties.<br />
4,4 ′ -Diaminodiphenylmethane was used as coupling agent in blends<br />
of maleated poly(propylene) <strong>and</strong> maleated styrene-butadiene-styrene triblock<br />
copolymers.<br />
82, 83<br />
16.4.1.2 Epoxy Monomers<br />
Multifunctional epoxy compounds are universal coupling agents for compatibilization<br />
of polymers such as poly(ethylene terephthalate) (PET) <strong>and</strong><br />
liquid crystalline polymers (LCP).<br />
36, 46<br />
16.4.1.3 Styrene/maleic anhydride Copolymer<br />
A commercially available styrene/maleic anhydride copolymer (SMA)<br />
with 8% MA is a highly effective compatibilizer for polymer blends of<br />
polyamide 6 (PA6) <strong>and</strong> poly(2,6-dimethyl-1,4-phenylene oxide) (PPO).<br />
SMA is miscible with PPO <strong>and</strong> tends to be dissolved in the PPO phase<br />
during the early stages of melt blending. The dissolved SMA can make<br />
reactive contacts of PA6 at the interface to form the desirable SMA-g-PA6<br />
copolymer. 31<br />
16.4.2 Vector Fluids<br />
To enhance the formation of the graft copolymer in compatibilization, vector<br />
fluids are introduced. A vector fluid is immiscible with both polymeric<br />
components of the two-phase blend. In the extruder it forms a thin <strong>and</strong><br />
low viscous film at the interphase of the immiscible polymers. It may have<br />
dissolved the peroxide. 84<br />
16.4.3 Poly(ethylene) <strong>and</strong> Polyamide 6<br />
16.4.3.1 Maleic anhydride Grafted Polyethylenes<br />
Various grades of poly(ethylene) grafted with maleic anhydride (PE-g-MA)<br />
<strong>and</strong> ethylene/acrylic acid copolymers (EAA) were used as compatibilizer
550 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
precursors for the reactive blending of low density PE (LDPE) with polyamide<br />
6 (PA6). Binary <strong>and</strong> ternary blends of compatibilizer, LDPE, <strong>and</strong><br />
polyamide were prepared in a Brabender mixer <strong>and</strong> were characterized by<br />
DSC, SEM, <strong>and</strong> solvent fractionation. PE-g-MA copolymers react more<br />
rapidly with PA than the EAA copolymers. The effectiveness depends critically<br />
on the microstructure <strong>and</strong> the molar mass of their PE backbones.<br />
Compatibilizers produced by the functionalization of LDPE are miscible<br />
with the LDPE component <strong>and</strong> scarcely available at the interface<br />
where reaction with PA is expected to occur. On the other h<strong>and</strong>, compatibilizers<br />
prepared from HDPE grades were immiscible with LDPE <strong>and</strong><br />
showed a better performance. The concentration of the carboxyl groups<br />
<strong>and</strong> the concentration of the succinic anhydride groups of the PE-g-MA<br />
compatibilizer play a minor role, in contrast to EAA copolymers.<br />
85, 86<br />
A low-viscosity maleated poly(ethylene) is ineffective in toughening<br />
nylon 6. This arises because of the propensity of poly(ethylene) to become<br />
continuous even when nylon 6 is the majority component. Higher viscosity<br />
maleated polyethylenes produce blends with high impact strength<br />
<strong>and</strong> excellent low temperature toughness over a range of compositions.<br />
Even poly(ethylene) materials with a low degree of anhydride functionality<br />
can generate blends with excellent impact properties. In ternary blends<br />
of nylon 6, maleated poly(ethylene), <strong>and</strong> nonmaleated poly(ethylene), the<br />
impact properties improve as the molecular weight of nylon 6 increases<br />
<strong>and</strong> the ratio of maleated poly(ethylene) to nonmaleated poly(ethylene) increases.<br />
87<br />
16.4.3.2 Epoxies<br />
In an ethylene-glycidylmethacrylate copolymer, the epoxy groups of the<br />
compatibilizer react quite easily during melt blending. Both the amine<br />
<strong>and</strong> the carboxyl end groups of PA react to result in CP-g-PA copolymers.<br />
These copolymers may be partially crosslinked. The efficiency of these<br />
compatibilizers is comparable to that of the ethylene-acrylic acid copolymers,<br />
but lower than that of a maleic anhydride-functionalized poly(ethylene).<br />
85, 86<br />
16.4.3.3 Diethylsuccinate<br />
Linear low density poly(ethylene) or ethylene propylene copolymer <strong>and</strong><br />
poly(ε-caprolactam) (PA6) can be compatibilized by reactive extrusion in
Compatibilization 551<br />
a Brabender mixer. The formation of a polyolefin-nylon grafted copolymer<br />
has been shown by selective solvent extraction of the product. The<br />
formation of the grafted copolymer has a substantial effect on the compatibilization<br />
of the two polymers.<br />
Differential scanning calorimetry shows a decrease of crystallization<br />
temperature <strong>and</strong> the enthalpy of PA6 crystallization. Scanning electron<br />
microscopy (SEM) micrographs show the size reduction of PA6 domains. 14<br />
16.4.3.4 Acrylic Acid<br />
Blends of polyamide 6 <strong>and</strong> polyolefins functionalized with acrylic acid,<br />
such as poly(ethylene)-PE-AA <strong>and</strong> poly(propylene)-PP-AA, exhibit changes<br />
in the crystallization behavior. Thermal analysis showed that in the case<br />
of blends, with functionalized polyolefin as a matrix, the following occurs:<br />
The crystallization of the polyamide 6 is spread <strong>and</strong> dramatically<br />
shifted toward lower temperatures, approaching that of the polyolefin component<br />
125 to 132°C. The major phase present is a polymorph γ-crystal of<br />
polyamide 6. When polyamide 6 is dispersed in the functionalized polyolefin<br />
matrix, the weight content of polyamide 6 γ-crystals increases up to<br />
three times relative to the analogous, non-compatibilized blends <strong>and</strong> up to<br />
approximately 16 times relative to the polyamide 6 homopolymer. These<br />
phenomena are explained by the reduction of the size of polyamide 6 dispersed<br />
particles, caused by the interactions between the functional groups<br />
of polyolefin <strong>and</strong> the polar groups in polyamide chain. The nucleation<br />
mechanism is changed due to the lack of heterogeneous nuclei in most<br />
small polyamide 6 droplets, which results in the enhanced γ-crystal formation.<br />
88<br />
16.4.4 Poly(ethylene-octene) <strong>and</strong> Poly(butylene terephthalate)<br />
Toughened poly(butylene terephthalate) (PBT) materials can be obtained<br />
by melt blending with poly(ethylene-octene) copolymer (PEO) <strong>and</strong> maleic<br />
anhydride grafted PEO (g-PEO) in a twin-screw extruder followed by injection<br />
molding at either 7 cm 3 /s or 17 cm 3 /s injection speed.<br />
The presence of either PEO or g-PEO did not influence either the<br />
nature of the PBT phase or the crystallization of PBT. Low injection speeds<br />
(7 cm 3 /s) <strong>and</strong> g-PEO provided the best mechanical response. Increasing<br />
levels of maleic anhydride in g-PEO led to a continuous overall decrease<br />
in the particle size.
552 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Super-tough poly(butylene terephthalate) (PBT)/ poly(ethyleneoctene)<br />
blends with an impact strength more than twenty-fold that of PBT<br />
are obtained using 2% poly(ethylene-co-glycidyl methacrylate) (EGMA)<br />
as a compatibilizer by extrusion or injection molding. Two percent EGMA<br />
is the minimum content required to reach maximum super-toughness that<br />
also corresponds to the maximum ductility. Partially reacted EGMA dissolves<br />
completely, mainly in the PBT-rich phase, up to 4% EGMA, at<br />
which point a crystalline EGMA phase appears. The blends consist of<br />
an amorphous PBT-rich phase with some mixed EGMA, a pure poly(ethylene-octene)<br />
amorphous phase, <strong>and</strong> a crystalline PBT phase. The blends<br />
show a fine particle size up to 20% poly(ethylene-octene) content. The<br />
inter-particle distance controls toughness in these PBT/PEO blends. The<br />
maximum toughness is very high, greater than 700 J/m, <strong>and</strong> was attained<br />
with 20% poly(ethylene-octene).<br />
39, 40, 89–91<br />
16.4.5 Poly(ethylene-octene) <strong>and</strong> Polyamide 6<br />
A maleated ethylene-octene copolymer promotes the toughness efficiency<br />
of PA6 remarkably. A blend with 20% ethylene-octene copolymer grafted<br />
with 1% MA reached a 20 times higher impact strength, i.e., 1000 J/m,<br />
than pure PA6 with 55 J/m impact strength. 92 The dispersed particle size<br />
was drastically reduced.<br />
16.4.6 Ethylene Acrylic Acid Copolymers <strong>and</strong> Polyamide 6<br />
In blends with polyamide 6 <strong>and</strong> ethylene acrylic acid copolymers, acrylic<br />
acid causes a compatibilizing effect between poly(ethylene) <strong>and</strong> polyamide<br />
components. The morphology of the blends <strong>and</strong> mechanical behavior thus<br />
changes. These effects are enhanced with increasing acrylic acid content in<br />
the copolymer <strong>and</strong> are attributed to interactions of hydrogen bonds between<br />
the acrylic acid group <strong>and</strong> the functional groups of the polyamide. Blends<br />
with a higher concentration of the terminal amino group in the polyamide<br />
suggest that these functional groups interact better with acrylic groups of<br />
the copolymer than the carboxylic groups. 93<br />
16.4.7 Sisal Fibers<br />
Sisal fibers show high strength <strong>and</strong> are obtained from the leaves of the<br />
sisal plant (agave sisalana). The leaves reach a length of 2 m. The plant
Compatibilization 553<br />
originates from central America <strong>and</strong> is now cultivated in East Africa <strong>and</strong><br />
East Asia.<br />
Acetylation of the sisal fiber improves the adhesion of the fiber to<br />
the polyolefin matrix. Acetylation of the sisal fiber enhances the tensile<br />
strength <strong>and</strong> modulus of the resulting composites, except in some cases.<br />
When the acetylated fiber is mixed with polyolefins, greater interactions<br />
with polyolefin <strong>and</strong> fiber takes place. These interactions enhance the stability<br />
of the composites. The thermal properties indicate mixing <strong>and</strong> molding<br />
temperatures between 160 <strong>and</strong> 230°C. 94<br />
16.4.8 Thermotropic Liquid Crystalline Polyesters<br />
Liquid crystalline polymers are polymers which in melt state lie between<br />
the boundaries of solid substances <strong>and</strong> liquids. The liquid crystalline structure<br />
is called a mesomorphic phase or an anisotropic phase because macroscopically<br />
in the melt state the liquid crystalline polymers are fluids. Microscopically<br />
they have a regular structure similar to that of crystals. The<br />
liquid crystalline polymers are called thermotropic (TLCP) if their anisotropy<br />
depends only on the temperature. The strength <strong>and</strong> stiffness of many<br />
thermoplastics can be substantially improved by blending them with thermotropic,<br />
main-chain liquid crystalline polymers. This is because the liquid<br />
crystalline polymers form fibers which orientate in the flow direction<br />
of the thermoplastic matrix melt. As a result there is an improvement of<br />
the mechanical properties, such as tensile strength <strong>and</strong> modulus of elasticity,<br />
of the thermoplastic in this direction. Often, the addition of the liquid<br />
crystalline polymer improves the heat resistance <strong>and</strong> dimensional stability<br />
of the thermoplastics <strong>and</strong> makes it easier to process them. 95<br />
The major limitation to the use of blends of TLCP in other polymers<br />
is the poor interfacial adhesion between the TLCP <strong>and</strong> matrix polymer.<br />
16.4.8.1 Physical Compatibilizer<br />
A physical compatibilizer for TLCP blends is the zinc salt of a sulfonated<br />
poly(styrene) ionomer. This ionomer can compatibilize blends of a<br />
hydroxybenzoate/hydroxynaphthonate liquid crystalline copolyester with<br />
poly(styrene), nylon 66 (PA66), bisphenol A, <strong>and</strong> poly(carbonate). 96–98
554 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
16.4.8.2 Transesterification<br />
Transesterification reactions have been used to improve the compatibility<br />
of a TLCP with polyesters or poly(carbonate)s. Maleated poly(propylene)<br />
can be used to improve the interfacial adhesion <strong>and</strong> mechanical properties<br />
of blends of a TLCP with polyolefins or polyamides<br />
16.4.8.3 Blends of Polyolefin <strong>and</strong> LCP<br />
A polymer blend of a polyolefin or a polyester polymer matrix <strong>and</strong> an<br />
aromatic main-chain liquid crystalline polymer can be compatibilized by<br />
a styrene-ethylene/butylene-styrene triblock copolymer that is functionalized<br />
with maleic anhydride. Olefin polymers functionalized with glycidyl<br />
methacrylate are suitable compatibilizers. 95<br />
By adding about 1 to 15% of a liquid crystalline polymer to the matrix<br />
polymer, e.g., poly(propylene), a decrease of the viscosity is obtained<br />
which enhances the processing. An example of a liquid crystalline polymer<br />
is a copolymer of hydroxynaphthoic acid <strong>and</strong> hydroxybenzoic acid. The<br />
compatibilizer is an ethylene-terpolymer containing glycidyl methacrylate.<br />
16.4.9 Ionomers <strong>and</strong> Ionomeric Compatibilizers<br />
16.4.9.1 Synthesis<br />
Ionomers formed by copolymerization of ethylene <strong>and</strong> methacrylic acid,<br />
either in the acid form or partially neutralized with zinc <strong>and</strong> sodium, have<br />
been blended with poly(3-hydroxybutyrate). The blending was achieved in<br />
an internal mixer <strong>and</strong> in a twin-screw extruder. During processing of the<br />
mixture of poly(3-hydroxybutyrate) <strong>and</strong> the sodium neutralized ionomer,<br />
a degradation accompanied with gas evolution took place. The best impact<br />
resistance was noticed in blends containing 30% of zinc neutralized<br />
ionomer, showing an increase of 53%. There is a strong indication that<br />
exchange reactions occur during the mixing process. 99<br />
16.4.9.2 Poly(ethylene terephthalate) <strong>and</strong> Polyamide 6<br />
An acrylic modified polyolefin-type ionomer with Zn 2+ is suitable to compatibilize<br />
blends of poly(ethylene terephthalate) (PET) <strong>and</strong> polyamide 6<br />
(PA6). Compatibilization is achieved with Zn 2+ levels higher than 10%.<br />
Good tensile <strong>and</strong> impact properties are obtained in quenched blends, while
Compatibilization 555<br />
in annealed samples the crystallization of the main components reduces the<br />
ductility. 48<br />
16.4.9.3 Poly(ethylene-co-vinyl alcohol) <strong>and</strong> Polyester<br />
Polymeric alloys of poly(ethylene-co-vinyl alcohol) (EVOH) with an amorphous<br />
copolyester (PETG) can be prepared using the sodium or the zinc<br />
ionomer of acrylic modified polyolefin ionomers. The sodium neutralized<br />
ionomer is a more efficient compatibilizer than the zinc salt. 100<br />
16.4.9.4 Poly(styrene) <strong>and</strong> Polyamide 6<br />
Poly(styrene-co-sodium acrylate) can be synthesized via emulsion polymerization.<br />
It is used as compatibilizer for poly(styrene) polyamide 6 mixtures.<br />
101<br />
16.4.9.5 Aromatic Polyester Blends<br />
Graft copolymers of wholly aromatic TLCP <strong>and</strong> ethylene-co-acrylic acid<br />
(EAA) ionomers can be produced using reactive processing. In particular,<br />
a wholly aromatic copolyester of 73% hydroxybenzoate (HBA) <strong>and</strong> 27%<br />
hydroxynaphthanoate (HNA) (Vectra A) <strong>and</strong> a wholly aromatic polyester<br />
from the foregoing compounds with the addition of terephthalic acid<br />
<strong>and</strong> hydroquinone was used. 102<br />
Blends of the ionomers with Vectra A were prepared by melt mixing<br />
in a Brabender Plasti-Corder EPL-5501 mixer at 300°C, likely due to an<br />
acidolysis reaction.<br />
Liquid crystalline polymer reinforced plastics are compounded from<br />
a mixture of poly(p-hydroxybenzoate) (PHB), poly(ethylene terephthalate)<br />
(PET) <strong>and</strong> poly(ethylene 2,6-naphthalate) (PEN). A fibrillar PHB structure<br />
is formed in-situ in the PEN/PET matrix under a high elongational flow<br />
field during melt spinning of the composite fibers.<br />
The PHB microfibril reinforced PEN/PET composite fibers exhibit<br />
a very low tensile modulus that can be explained by the assumption of a<br />
very large number of PHB microfibrils, by the Takayanagi model. 103<br />
16.4.9.6 Aromatic Polyether Blends<br />
Poly(2,6-dimethyl-1,4-phenylene oxide) (PPO) <strong>and</strong> poly(2,6-dichloro-<br />
1,4-phenylene oxide) (PDClPO) can be compatibilized with sulfonated
556 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
poly(styrene). 104 Neutralized sulfonated poly(styrene) has a high miscibility<br />
with both PPO <strong>and</strong> PDClPO.<br />
16.4.10 Poly(styrene)<br />
16.4.10.1 Poly(styrene) <strong>and</strong> Polyamide 6,6<br />
Poly(styrene)s <strong>and</strong> nylons have been produced commercially by polymerization<br />
in an extruder.<br />
Blends of polyamide <strong>and</strong> poly(styrene) are attractive because the incorporation<br />
of various functional groups such as maleic anhydride, glycidyl<br />
methacrylate, <strong>and</strong> acrylic acid into poly(styrene) is comparatively<br />
simple. Functionalized poly(styrene) can be used as compatibilizer for<br />
PA/poly(2,6-dimethyl-1,4-phenylene oxide) (PPO) blends, because it is<br />
miscible with PPO. Phthalic anhydride-terminated poly(styrene) (PS-PAH)<br />
<strong>and</strong> styrene-maleic anhydride copolymer (SMA) is a compatibilizer at low<br />
loadings of smaller than 10% in blends of 70%polyamide 66 (PA66) <strong>and</strong><br />
30% poly(styrene) (PS). 37<br />
16.4.10.2 Poly(styrene/acrylonitrile) <strong>and</strong> Polyamide 6<br />
Blends of polyamide 6 (PA6) <strong>and</strong> a copolymer of styrene/acrylonitrile<br />
(SAN) can be compatibilized by an imidized acrylic polymer (IA) or a<br />
styrene/acrylonitrile/maleic anhydride terpolymer (SANMA). 105<br />
The addition of IA causes the phase inversion composition to shift<br />
to a higher nylon 6 volume fraction. Without any compatibilizer, the phase<br />
inversion occurs at a volume fraction of about 0.48 of polyamide 6. By the<br />
addition of IA, the phase inversion composition shifts to a higher polyamide<br />
6 volume fraction.<br />
For uncompatibilized blends, the relationship between particle size<br />
<strong>and</strong> composition is symmetric about the phase inversion composition,<br />
whereas, blends compatibilized with IA show an intense asymmetric behavior,<br />
i.e., SAN dispersed particles in a nylon 6 matrix are quite small,<br />
while nylon 6 particles in a SAN matrix are much larger <strong>and</strong> are elongated.<br />
106 Using Wu’s equation, predicting the dispersed phase particle size,<br />
it is suggested that the viscosity increase of a nylon 6 phase due to the<br />
formation of graft polymers may affect the asymmetric behavior. However,<br />
the predicted asymmetry was less pronounced than the experimentally<br />
observed asymmetry.
Compatibilization 557<br />
IA also results in a significant increase of the nylon 6 phase viscosity<br />
due to the in-situ formation of graft polymers during the melt processing.<br />
The significant change in the ratios of the phase viscosity is to the formation<br />
of a PA/IA graft polymer. The formation of the graft polymer may be<br />
partially responsible for the shift of the phase inversion composition observed,<br />
when IA is added. IA does not stabilize the morphology near the<br />
phase inversion composition, however, it is effective at compositions where<br />
either of the components would form a clearly defined dispersed phase.<br />
The addition of SANMA only slightly changes the phase inversion<br />
composition to a lower nylon 6 volume fraction. The phase viscosity nylon<br />
6 is only slightly increased. The addition of IA or SANMA does not<br />
increase the viscosity of the SAN phase. 105<br />
16.4.10.3 Poly(styrene) <strong>and</strong> Ethylene/propylene Rubber<br />
Blends of poly(styrene) (PS) <strong>and</strong>ethylene/propylene rubber (EPR) can be<br />
compatibilized by various block copolymer interfacial modifiers by melt<br />
processing. 50<br />
16.4.10.4 SAN <strong>and</strong> Poly(carbonate)<br />
The nitrile groups in SAN can be converted by 1,3-aminoethylpropanediol<br />
or by o-aminophenol into oxazoline groups. Dibutyltin oxide is an effective<br />
catalyst. Thus, ethyl hydroxymethyl oxazoline (EHMOXA) <strong>and</strong> benzoxazole<br />
(BenzOXA), respectively, were introduced in the polymer. 107, 108 The<br />
modified SAN was reacted with poly(carbonate). The SAN modified with<br />
reacted EHMOXA exhibited crosslinked structures when reacted with PC,<br />
whereas the BenzOXA-modified SAN showed a compatibilization without<br />
crosslinking.<br />
16.4.10.5 SAN <strong>and</strong> EPDM<br />
Free-radical initiators such as 2,5-dimethyl-2,5-di(tert-butylperoxy)hexane,<br />
2,5-dimethyl-2,5-di(tert-butylperoxy)-3-hexyne, α,α ′ -di(tert-butylperoxy)diisopropylbenzene,<br />
<strong>and</strong> 2,2 ′ -azobis(2-acetoxy)propane were used<br />
for the reactive blending of styrene/acrylonitrile copolymer (SAN) <strong>and</strong> ethylene-propylene-diene<br />
terpolymer (EPDM). 109 A dominant grafting reaction<br />
was observed in blends using α,α ′ -di(tert-butylperoxy)diisopropylbenzene<br />
as initiator.
558 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
16.4.11 Polyolefins/Poly(ethylene oxide)<br />
Personal care products, such as baby diapers, sanitary napkins, adult diapers,<br />
etc., are generally constructed from a number of different components<br />
<strong>and</strong> materials. Such articles typically have some portion, usually the backing<br />
layer, that is composed of a film constructed from a liquid repellent<br />
material.<br />
This repellent material is appropriately constructed to minimize or<br />
prevent the exuding of the absorbed liquid from the article <strong>and</strong> to obtain<br />
greater utilization of the absorbent capacity of the product. The liquid<br />
repellent film commonly used includes plastic materials such as poly(ethylene)<br />
films.<br />
Polymer blends of polyolefins <strong>and</strong> poly(ethylene oxide) are melt<br />
processable but exhibit very poor mechanical compatibility. This poor mechanical<br />
compatibility is particularly manifested in blends having greater<br />
than 50% of polyolefin. Generally the film is not affected by water since<br />
typically the majority phase, i.e., polyolefin, will surround <strong>and</strong> encapsulate<br />
the minority phase, i.e., the poly(ethylene oxide).<br />
The encapsulation of the poly(ethylene oxide) effectively prevents<br />
any degradability <strong>and</strong>/or flushability advantage that would be acquired by<br />
using poly(ethylene oxide). An inverse phase composition, characterized<br />
by a continuous phase of poly(ethylene oxide) <strong>and</strong> a dispersed phase of<br />
polyolefin, can be produced by reactive extrusion.<br />
The components, the polyolefin, poly(ethylene oxide), poly(ethylene<br />
glycol)methacrylate or 2-hydroxyethyl methacrylate <strong>and</strong> the initiator<br />
2,5-dimethyl-2,5-di(tert-butylperoxy)hexane, i.e., Lupersol 101 or Interox<br />
DHBP can be premixed before heating, <strong>and</strong> blending to produce<br />
an inverse phase composition. Alternatively, the components may be added<br />
simultaneously or separately to a reaction vessel for melting <strong>and</strong> blending.<br />
Ideally, the polyolefin <strong>and</strong> poly(ethylene oxide) should be melt blended before<br />
adding monomer or initiator. The monomer <strong>and</strong> initiator may be added<br />
to the molten polymers separately or combined in a solution comprised of<br />
the monomer <strong>and</strong> the initiator.<br />
In a reactive extrusion process, it is desirable to feed the polyolefin<br />
<strong>and</strong> poly(ethylene oxide) into an extruder before adding monomer further<br />
down the extruder <strong>and</strong> adding initiator even further down the extruder. This<br />
sequence facilitates mixing of the monomer or mixture of monomers into<br />
the polymers before the initiator is added <strong>and</strong> radicals are created. 110
Compatibilization 559<br />
16.4.12 Poly(phenylene sulfide)/Liquid Crystalline <strong>Polymers</strong><br />
The in-situ compatibilization of poly(phenylene sulfide) (PPS) with aromatic<br />
thermotropic liquid crystalline polymers occurs via a transesterification<br />
reaction between the carboxyl groups of a modified poly(phenylene<br />
sulfide) <strong>and</strong> the ester linkages of the liquid crystalline polymer. 111<br />
16.4.13 LDPE/Thermoplastic Starch<br />
Thermoplastic starch (TPS), in contrast to dry starch, is capable of flow.<br />
When thermoplastic starch is mixed with other synthetic polymers, these<br />
blends behave in a manner similar to conventional polymer blends. A onestep<br />
combined twin-screw/single-screw extrusion setup is suitable for the<br />
melt-melt mixing of LDPE <strong>and</strong> thermoplastic starch.<br />
Glycerol is used as a plasticizer for starch in the content range of 29<br />
to 40%. It is possible to manufacture a continuous TPS (highly interconnected)<br />
<strong>and</strong> co-continuous polymer/TPS blend extruded ribbon. This ribbon<br />
has excellent mechanical properties in the absence of any interfacial<br />
modifier <strong>and</strong> despite the high levels of immiscibility in the polar-nonpolar<br />
TPS-PE system. A high degree of transparency is maintained over the entire<br />
concentration range due to the similar refractive indices of PE <strong>and</strong> TPS<br />
<strong>and</strong> the virtual absence of interfacial microvoiding.<br />
This material also has the benefit of containing large quantities of a<br />
renewable resource <strong>and</strong> hence represents a more sustainable alternative to<br />
pure synthetic polymers. 112<br />
16.4.14 PE <strong>and</strong> EVA<br />
Saponified ethylene-vinyl acetate copolymers in general have good oxygen<br />
barrier properties, mechanical strength, etc. <strong>and</strong>, as such, have found<br />
application in many uses such as film, sheet, container material, <strong>and</strong> textile<br />
fiber. However, this saponified copolymer gives rise to a variation in<br />
product thickness in the molding process for manufacture of film or sheet,<br />
with the consequent decrease in the marketability of the product. Because<br />
of the deficiency in stretchability <strong>and</strong> flexibility, it gives rise to uneven<br />
stretching in deep-drawing <strong>and</strong> other processes involving a stretching force<br />
or pinholes in use of the product, thus imposing serious limitations on its<br />
application as a packaging raw material.
560 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Blends of saponified ethylene-vinyl acetate copolymer <strong>and</strong> an ethylene<br />
copolymer, such as low density poly(ethylene), linear low density<br />
poly(ethylene), ethylene-vinyl acetate copolymer, or an ethylene-acrylic<br />
ester copolymer show improved properties, however they need a compatibilizer.<br />
The compatibilizer can consist of a graft polymer, obtainable by<br />
grafting an ethylenically unsaturated carboxylic acid such as acrylic acid,<br />
or methacrylic acid, to a polyolefin resin <strong>and</strong> reacting this carboxylic acid<br />
or derivative thereof with a polyamide oligomer or polyamide. The compatibilizer<br />
is added in amounts of 0.5 to 10%. 113<br />
The compatibility of the blend is markedly improved <strong>and</strong> the material<br />
shows an excellent oxygen barrier property <strong>and</strong> improvements in<br />
stretchability, film thickness, <strong>and</strong> flexibility which are deficient in the saponified<br />
ethylene-vinyl acetate copolymer alone.<br />
16.4.15 SBR <strong>and</strong> EVA<br />
Poly(chloroprene)/EVA blends are miscible in all proportions. However,<br />
other EVA/rubber blends are incompatible because of the strong differences<br />
in chemical structure, polarity, etc. EVA copolymers are potential<br />
interesting partners for blends with unsaturated elastomers because of their<br />
excellent ozone resistance, weather resistance, <strong>and</strong> mechanical properties.<br />
Blends of a styrene/butadiene copolymer <strong>and</strong> an ethylene/vinyl acetate<br />
copolymer (SBR/EVA) can be compatibilized with a mercapto-modified<br />
EVA (EVALSH). This polymer promotes the bonding between the SBR<br />
phase <strong>and</strong> the EVALSH through a chemical reaction between the mercapto<br />
groups of the reactive compatibilizing agent <strong>and</strong> the double bond of the<br />
unsaturated rubber. 114, 115 Blends of SBR <strong>and</strong> EVA find important applications<br />
in the footwear industry<br />
16.4.16 NBR <strong>and</strong> EPDM<br />
The reactive compatibilization of NBR/EPDM blends can be achieved by<br />
the combination of mercapto <strong>and</strong> oxazoline groups. 116, 117 Mercapto-modified<br />
EPDM copolymers are blended with oxazoline-functionalized NBR.<br />
Insoluble material was found in non-vulcanized blends which suggested<br />
a reactive compatibilization mechanism. Namely, the mercapto groups are<br />
able to react with the carbon-carbon double bonds of the high diene rubber.<br />
This results in a good interaction between the phases. A functionalization<br />
of the nitrile rubber with epoxy groups also increases performance. 118–120
Compatibilization 561<br />
16.4.17 NBR <strong>and</strong> PA6<br />
The compatibilization of blends of polyamide 6 with a nitrile butadiene<br />
rubber consists of two steps: 121<br />
1. Modification of the nitrile groups of the rubber into oxazoline in<br />
the melt through condensation of ethanolamine with loss of ammonia.<br />
2. Melt mixing the modified rubber with the polyamide.<br />
16.4.18 Poly(carbonate)–Poly(vinylidene fluoride) Blends<br />
Immiscible PC/PVDF blends can be compatibilized by the addition of<br />
poly(methyl methacrylate) (PMMA). PMMA is miscible with PVDF <strong>and</strong><br />
is compatible to PC. When PVDF is premixed with 40% PMMA, the interfacial<br />
tension with PC is substantially decreased <strong>and</strong> the interfacial adhesion<br />
is increased. Actually, the original PVDF/PC interface is replaced<br />
by the more favorable PMMA/PC. 122 The PMMA content in PVDF can be<br />
decreased further, by enhancing the PMMA/PC interactions.<br />
When the PMMA contains acid groups, the carbonate bonds of PC<br />
can be acidolyzed according to the mechanism of Figure 16.3. However,<br />
the acidolysis reaction does not proceed, significantly, below 240°C. The<br />
neutralization of the carboxylic acid groups by metal cation could contribute<br />
to the catalysis of the acidolysis reaction. Zinc cations are known for<br />
coordinative interaction with electron donating heteroatoms <strong>and</strong> are active<br />
in catalyzing the acidolysis grafting reaction. For this reason, a tailor-made<br />
compatibilizer has been designed that includes the desired issues.<br />
Poly(carbonate) <strong>and</strong> Poly(vinylidene fluoride) (PVDF) are melt<br />
blended with a r<strong>and</strong>om copolymer of methyl methacrylate <strong>and</strong> 6 mol-%<br />
of acrylic acid [poly(MMA-co-AA)] as compatibilizer. The copolymer is<br />
neutralized by Zn 2+ . Poly(carbonate) reacts in solution at 240°C with the<br />
compatibilizer. The reaction leads to the grafting of PC onto the copolymer<br />
whether it is neutralized or not neutralized. In the melt at 235°C, the<br />
grafting reaction occurs only when the copolymer is at least partly neutralized.<br />
42<br />
16.4.19 Bisphenol A-poly(carbonate) <strong>and</strong> ABS Copolymers<br />
An amine-functional styrene/acrylonitrile (SAN/amine) polymer is a reactive<br />
compatibilizer for blends of bisphenol A-poly(carbonate) <strong>and</strong> acryl-
562 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
CH 3<br />
CH 2 C<br />
C<br />
O OH<br />
+<br />
O C<br />
O<br />
O<br />
O<br />
CH 3<br />
C<br />
C<br />
O<br />
CH 2<br />
CO 2<br />
OH<br />
Figure 16.3: Acidolysis of a Poly(carbonate) by a Pendent Polymeric Acid Group
Compatibilization 563<br />
onitrile/butadiene/styrene (PC/ABS) copolymers. Amine groups react<br />
rapidly with poly(carbonate).<br />
Secondary-amine-functional SAN polymers can be synthesized by<br />
the derivatization of an SAN/MA terpolymer with a difunctional amine,<br />
such as 1-(2-aminoethyl)piperazine (AEP). The anhydride forms with the<br />
amine the amic acid intermediate. A thermally or chemically mediated<br />
dehydration yields the imide. The compatibilization reaction occurs by<br />
the reaction of the secondary amine group attached to this SAN backbone<br />
with the poly(carbonate). The poly(carbonate) grafts are attached to the<br />
SAN backbone by a urethane linkage. 123<br />
Most polyurethanes are not stable at processing temperatures above<br />
200°C. However, urethanes resulting from piperazine or other secondary<br />
amines do not undergo the dissociation reaction because they lack a labile<br />
hydrogen.<br />
16.4.20 Kevlar<br />
Poly(p-phenylene terephthalamide) (Kevlar) is used as reinforcing material<br />
in composite systems with a polyolefin-based thermoplastic elastomer.<br />
With increasing amounts of Kevlar in the composite, the low-strain modulus<br />
<strong>and</strong> tensile strength increases, while the elongation at break decreases<br />
sharply. To improve mechanical properties of the composite, a hydrolysis<br />
of the Kevlar surface can be employed. Further, maleic anhydridegrafted-poly(propylene)<br />
(MA-g-PP) is used as a reactive compatibilizer.<br />
The treated Kevlar greatly improves the low-strain modulus, the tensile<br />
strength, <strong>and</strong> elongation at break of the composite.<br />
In such a composite the interfacial adhesion of the fiber <strong>and</strong> the matrix<br />
might increase, as well as the effective volume fraction of the fiber,<br />
thereby resulting in a better distribution of the stress along the reinforcing<br />
fiber. 124<br />
16.4.21 Polyamides<br />
The amino group of polyamides easily undergoes reactions with anhydrides,<br />
acids, esters, <strong>and</strong> oxazolines. The rate of these reactions is sufficient<br />
for applications in reactive extrusion. The polyolefins used are modified<br />
with maleic anhydride, glycidylmethacrylate <strong>and</strong> acrylic acid <strong>and</strong> acrylic<br />
esters.
564 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
The amide linkage in polyamide is substantially less reactive than<br />
the terminal primary amino group. On the other h<strong>and</strong>, the concentration<br />
of amide linkages is much higher than amino end groups. The reaction of<br />
an amide with an anhydride results in cleavage of the polyamide chain. It<br />
was shown that the reaction of the amine with the anhydride is dominant<br />
for graft formation of polyamide with polyolefins. 125–127<br />
A copolymer of ethylene <strong>and</strong> acrylic acid (EAA) is an effective compatibilizer<br />
precursor for PA/LDPE blends. However, the in-situ formation<br />
of copolymers of PA grafted onto EAA is slow. A bis-oxazoline compound,<br />
such as 2,2 ′ -(1,3-phenylene)bis(2-oxazoline) (PBO) is a promoter<br />
for the formation of PA-g-EAA copolymers. The oxazoline rings of PBO<br />
react under the conditions of preparation of the blends in bridging reactions.<br />
Further, the addition of the bis-oxazoline causes some reduction of<br />
the degree of crystallinity of the PA phase of these blends. 16<br />
In order to compatibilize polyamide 12,12 with polyamide 6, a maleated<br />
triblock copolymer of styrene-(ethylene-co-butene)-styrene (SEBSg-MA)<br />
was successful. At a ratio of polyamide 12,12 to polyamide 6<br />
of 30/70, supertoughness was achieved by the addition of 15% SEBSg-MA.<br />
128<br />
16.4.21.1 Ethylene/propylene Elastomers<br />
In melt blending of nylon 6 <strong>and</strong> ethylene/propylene rubber grafted with<br />
maleic anhydride (EPR-g-MA), for certain compositions, nylon 6 forms<br />
finely dispersed particles due to the reaction of the polyamide amine end<br />
groups with the grafted maleic anhydride. Under these circumstances, the<br />
polyamide has the potential to reinforce the elastomer matrix. Further,<br />
the addition of magnesium oxide causes significant improvement in tensile<br />
properties of these blends. 129<br />
16.4.22 Polyethers<br />
Poly(phenylene ether)s (PPE) constitute a family of high performance engineering<br />
thermoplastics possessing outst<strong>and</strong>ing properties, such as relatively<br />
high melt viscosities <strong>and</strong> softening points, which make them useful<br />
for many commercial applications.<br />
However, high temperatures are required to soften poly(phenylene<br />
ether)s which cause instability <strong>and</strong> changes in the polymer structure. Further,<br />
PPE polymers tend to degrade <strong>and</strong> to grow dark during melt process-
Compatibilization 565<br />
ing. In order to improve molding properties <strong>and</strong> impact strength, blends of<br />
poly(phenylene ether)s with styrene resins have been employed. 130<br />
Polyethers will have hydroxy end groups, if they are not derivatized.<br />
Polyethers with amino end groups <strong>and</strong> carboxyl end groups <strong>and</strong> various<br />
nonreactive chain groups are commercially available.<br />
Blends based on poly(2,6-dimethyl-1,4-phenylene ether) (PPE) <strong>and</strong><br />
poly(butylene terephthalate) (PBT) are mutually incompatible. The phase<br />
morphologies obtained during blending of these polymers are generally<br />
unstable. When PPE is functionalized selectively, in-situ compatibilization<br />
during processing is possible. PPE with hydroxyalkyl, carboxylic acid,<br />
methyl ester, amino <strong>and</strong> tert-BOC protected amino end groups are active as<br />
compatibilizers. These reactive groups are positioned either in the middle<br />
of the chain or as end groups. PPEs with carboxylic acid end groups are<br />
most efficient in compatibilizing the blends with PBT. Promoters, which<br />
catalyze or take part in the coupling between PBT <strong>and</strong>/or functionalized<br />
PPEs, are triphenyl phosphite (TPP), sodium stearate, titanium (IV) isopropoxide,<br />
<strong>and</strong> epoxy resins. 131<br />
Polyolefins, particularly poly(ethylene) (PE), even when added in<br />
small amounts, can noticeably change some characteristics of the PPE,<br />
such as impact strength <strong>and</strong> solvent resistance. PE acts as a plasticizer for<br />
PPE, <strong>and</strong> the resulting blends are endowed with enhanced workability <strong>and</strong><br />
better surface properties.<br />
In order to increase the amount of compatible PE in PPE-PE blends,<br />
styrene (co)polymers or block copolymers of styrene <strong>and</strong> a conjugated<br />
diene as compatibilizers can be added. Another possibility is the use of<br />
PPE-PE copolymers. These copolymers serve as compatibilizers for PPE<br />
<strong>and</strong> PE.<br />
Poly(phenylene ether)-grafted polyolefin can be obtained by reacting<br />
a glycidylated PPE with a polyolefin having anhydride groups or by<br />
reacting a poly(phenylene ether) having anhydride groups with a glycidylated<br />
polyolefin, respectively. 132<br />
In particular, PPE can be end-capped with epoxychlorotriazine.<br />
PPE-PE graft copolymers can also be obtained by melt kneading a poly-<br />
(phenylene ether), modified with maleic anhydride <strong>and</strong> a polyolefin, modified<br />
with maleic anhydride in the presence of a binder such as phenylene<br />
diamine. 133<br />
Further, poly(phenylene ether)-poly(ethylene) copolymer blends can<br />
be prepared by reactive melt blending of poly(phenylene ether) or an ester
566 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
end-capped poly(phenylene ether) with an ethylene/acrylic acid copolymer.<br />
130 End-capped PPE is generally prepared by the reaction of a poly-<br />
(phenylene ether) with carboxylic anhydride in the presence of a catalyst.<br />
16.4.23 Polyurethane <strong>and</strong> Poly(ethylene terephthalate)<br />
The compatibility behavior of polyurethane (PU)/poly(ethylene terephthalate)<br />
(PET) is of interest because of the following considerations: 134<br />
1. PET is a widely used thermoplastic with a poor impact resistance<br />
when it is injection molded. The combination with PU promises<br />
to raise its impact strength.<br />
2. The polymer pair may be compatible since the carbonyl groups of<br />
the polyester may interact with the hydrogens of NH groups of the<br />
polyurethane.<br />
Polymeric alloys with good mechanical properties over the complete<br />
composition range are obtained by melt blending a polyester polyurethane<br />
(PU) <strong>and</strong> poly(ethylene terephthalate) (PET). During the mixing, ester-amide<br />
reactions take place which cause an in-situ reactive compatibilization<br />
without a catalyst. 134<br />
16.5 FUNCTIONALIZATION OF END GROUPS<br />
16.5.1 Mechanisms<br />
16.5.1.1 Anionic Polymerization<br />
Poly(styrene) with hydroxyl end groups can be prepared by anionic polymerization.<br />
After the propagation reaction, the living polystyryl anions are<br />
reacted with ethylene oxide by a ring opening reaction. A poly(styrene)<br />
with hydroxyl end groups can be reacted with polyolefins that are modified<br />
with maleic anhydride.<br />
The process can be conducted either in solution or by the extrusion<br />
of a mixture of the two modified polymers in a single-screw extruder. A<br />
high yield of graft copolymer is obtained.<br />
Poly(ethylene-co-methyl acrylate) can be transesterified with hydroxy-terminated<br />
poly(styrene) in a batch mixer. The final conversion <strong>and</strong><br />
the rate of the reaction are strongly dependent on the molecular weight of<br />
the poly(styrene). 135
Compatibilization 567<br />
The transesterification of ethylene <strong>and</strong> alkyl acrylate copolymers<br />
with 3-phenyl-1-propanol (PPOH) as a model substance was studied in<br />
1,2,4-trichlorobenzene solution <strong>and</strong> in the melt. Among various catalysts,<br />
dibutyltin dilaurate (DBTDL) <strong>and</strong> dibutyltin oxide (DBTO) show the highest<br />
activities. In the melt, in a semi-open batch mixer at temperatures between<br />
170 <strong>and</strong> 190°C, the equilibrium is totally shifted to the product side<br />
due to effective removal of the lighter alcohols generated from the reaction.<br />
136<br />
16.5.1.2 Living Free-Radical Polymerization<br />
Free-radical polymerization has not been regarded as a useful technique<br />
in the synthesis of end-functional polymers, however, the advent of living<br />
radical polymerization has changed the situation. End-functional polymers<br />
can now be produced with this technique. 137–139<br />
Living free-radical polymerization is a comparatively recent method<br />
for controlled free-radical polymerization. It combines the advantages of<br />
conventional free-radical polymerization (simple production process, low<br />
cost, <strong>and</strong> a wide range of monomers) with those of living polymerization<br />
(polymers of a defined structure, molecular weight, molecular weight distribution,<br />
<strong>and</strong> end group functionality).<br />
Precise control of the free-radical polymerization is achieved by reversible<br />
chain termination/blocking (endcapping) after each growth stage.<br />
The equilibrium concentration of the actively polymerizing chain ends at<br />
this point is so low in comparison with the equilibrium concentration of the<br />
blocked (dormant) chain ends that termination <strong>and</strong> transfer reactions are<br />
largely suppressed in comparison with the growth reaction. Since endcapping<br />
is a reversible reaction, all the chain ends remain living providing that<br />
no terminating reagent is present. This allows the control of the molecular<br />
weight, a narrow molecular weight distribution, <strong>and</strong> purposeful functionalization<br />
of the chain end by terminating reagents. Various techniques of<br />
living free-radical polymerization are known: 140<br />
• Iniferter Method<br />
• Reversible Chain Termination<br />
• Atom Transfer Radical Polymerization.<br />
Iniferter Method. The iniferter method uses a class of free radical initiators<br />
which can enter into initiation, transfer, <strong>and</strong> reversible termination re-
568 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
actions, e.g., tetraalkylthiuram disulfides which are photolytically cleaved<br />
<strong>and</strong> activated. In this manner, it is possible to produce polymers having<br />
dithiocarbamate end groups that may be reactivated by irradiation.<br />
Poly(isoprene-butyl acrylate) block copolymers have been prepared<br />
by the iniferter method. These block copolymers were used as compatibilizers<br />
in blends of natural rubber <strong>and</strong> acrylic rubber. 141<br />
Reversible Chain Termination. The principle of reversible chain termination<br />
uses free radicals based in linear or cyclic nitroxides such as<br />
tetramethyl-1-piperidinyloxy (TEMPO). If this nitroxide is reacted with<br />
a reactive carbon radical capable of initiating a free radical vinyl polymerization<br />
reaction, a reversibly cleavable C–O bond is formed which, when<br />
subjected to moderate heating, is capable of bringing about polymerization<br />
by insertion of vinyl monomers between the nitroxide <strong>and</strong> carbon radical.<br />
After each monomer addition, the newly formed radical is scavenged<br />
by the nitroxide. This reversibly blocked chain end may then insert further<br />
monomer molecules. Reversible termination with nitroxide may use, for<br />
example, a combination of dibenzoyl peroxide (BPO) <strong>and</strong> TEMPO.<br />
Atom Transfer Radical Polymerization. Another approach is atom<br />
transfer radical polymerization (ATRP). Here, a transition metal complex<br />
compound ML x abstracts a transferable atom or group of atoms X, for<br />
example, Cl <strong>and</strong> Br, from an organic compound RX to form an oxidized<br />
complex compound ML x X <strong>and</strong> an organic radical R·, which undergoes an<br />
addition reaction with a vinyl monomer Y to form the carbon radical RY ·.<br />
This radical is capable of reacting with the oxidized complex compound,<br />
transferring X to RYX <strong>and</strong> regenerating ML x , which can initiate a new<br />
ATRP reaction <strong>and</strong> thus a further growth stage. The actively polymerizing<br />
species RY· is thus reversibly blocked by the abstractable group X with<br />
the assistance of the transition metal compound, which makes the redox<br />
process possible. 140<br />
Telechelic <strong>Polymers</strong>. Telechelic substances are generally defined as linear<br />
oligomers or low molecular weight linear polymers having functional<br />
groups on both chain ends. Living free-radical polymerization is a suitable<br />
method to produce such telechelic polymers. For example, telechelic<br />
polyacrylates can participate in crosslinking, chain extension or coupling<br />
reactions conventionally used in lacquer chemistry. Therefore, they are of
Compatibilization 569<br />
great interest for use in the lacquer industry. Telechelic polymers can be<br />
produced by atom transfer radical polymerization with a suitable functionalizing<br />
reagent that has a polymerizable double bond. 140 Examples for the<br />
production of telechelic polymers are given in Table 16.3.<br />
16.5.1.3 Friedel-Crafts Alkylation of Poly(styrene) <strong>and</strong> Polyolefin<br />
Poly(styrene) is subject to a Friedel-Crafts alkylation with AlCl 3 as catalyst.<br />
A PP macrocarbocation is chemically bonded to the PS benzene ring<br />
by aromatic electrophilic substitution. 142<br />
In-situ compatibilization of polyolefin <strong>and</strong> poly(styrene) is achieved<br />
by Friedel-Crafts alkylation through a reactive extrusion process. Styrene<br />
monomer is used as co-catalyst . A two-step procedure gives better results<br />
than a one-step procedure. The method has the potential to recycle mixed<br />
wastes from polyolefins <strong>and</strong> poly(styrene). 143 In the case of blends of PS<br />
<strong>and</strong> LLDPE it was proven that the LLDPE segments were grafted onto the<br />
para position of the benzene rings of PS. 144<br />
16.5.2 Amino-terminated Nitrile Rubber<br />
Amino-terminated nitrile rubber reacts with maleic anhydride grafted poly-<br />
(propylene).<br />
16.5.3 Functionalization of Olefinic End Groups of Poly(propylene)<br />
Various end groups, such as anhydride, carboxylic acid, alcohol, thiol, silane,<br />
<strong>and</strong> borane can be introduced into the terminal unsaturations of poly-<br />
(propylene) with a metallocene catalyst. 145<br />
16.5.3.1 Maleated Poly(propylene)<br />
Maleated poly(propylene) is not a copolymer of maleic anhydride <strong>and</strong><br />
propylene, such that the maleic anhydride moiety is predominantly in the<br />
backbone of the copolymer. Suitable monomers for preparing functionalized<br />
poly(propylene) are<br />
• Olefinically unsaturated monocarboxylic acids, e.g., acrylic acid<br />
or methacrylic acid, <strong>and</strong> the corresponding tert-butyl esters, e.g.,<br />
tert-butyl acrylate or tert-butyl methacrylate,
570 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 16.3: Production of Telechelic <strong>Polymers</strong> 140<br />
Example No. 1 2 3 4 5 6<br />
Composition<br />
CuCl/CuBr 49 25 25 20 9 30<br />
Bipyridin 234 117 117 94 43 140<br />
Methyl methacrylate 939 500 196 400 187 100<br />
n-Butyl acrylate 894 128<br />
2-Ethylhexyl acrylate 184<br />
Allyl alcohol 582 135 171<br />
AMPC 175 112 153 344<br />
HCPA 246 61<br />
NHCPA 50<br />
BIAE<br />
α,α-Dichlorotoluene 32 15 48<br />
Butyl acetate 710 440 440 440 180 440<br />
Reaction time [h] 60 20 21 24 22 21<br />
Reaction temp. [°C] 130 130 130 130 130 130<br />
M n (GPC) 1900 6300 2500 3000 3100 2000<br />
M w /M n (GPC) 1,25 1,14 1,39 1,43 1,25 1,43<br />
Functionality a 1,8 1,9 1,97 1,95 >1.6 >1,8<br />
AMPC Allyl-N-(4-methyl-phenyl)carbamate<br />
HCPA 4-Hydroxybutyl-2-chloro-2-phenylacetate<br />
NHCPA N-(2-Hydroxyethyl)-2-chloro-2-phenylacetamide<br />
BIAE 2-Bromoisobutyric acid ethylester<br />
a<br />
with respect to end groups<br />
Example 1:<br />
Initiator + end capping with allyl alcohol<br />
Examples 2 <strong>and</strong> 3: OH-functional initiator + end capping with<br />
the phenylurethane derivative of allyl alcohol<br />
Examples 4 <strong>and</strong> 6: Double end capping with the phenylurethane<br />
derivative of allyl alcohol<br />
Example 5:<br />
Double end capping with allyl alcohol.
Compatibilization 571<br />
• Olefinically unsaturated dicarboxylic acids, e.g., fumaric acid,<br />
maleic acid, <strong>and</strong> itaconic acid <strong>and</strong> the corresponding di-tert-butyl<br />
esters, e.g., mono or di-tert-butyl fumarate <strong>and</strong> mono or di-tertbutyl<br />
maleate,<br />
• Olefinically unsaturated dicarboxylic anhydrides, e.g., maleic<br />
anhydride, sulfo- or sulfonyl-containing olefinically unsaturated<br />
monomers, e.g., p-styrenesulfonic acid, 2-methacrylamide-<br />
2-methylpropenesulfonic acid or 2-sulfonyl(meth)acrylate,<br />
• Oxazolinyl-containing olefinically unsaturated monomers, e.g.,<br />
vinyloxazolines <strong>and</strong> vinyloxazoline derivatives, <strong>and</strong><br />
• Epoxy-containing olefinically unsaturated monomers, e.g., glycidyl<br />
(meth)acrylate or allyl glycidyl ether.<br />
The most common monomer for preparing functionalized poly(propylene)<br />
is maleic anhydride. Maleated poly(propylene) is commercially<br />
available.<br />
16.5.3.2 Amine Functions in Poly(propylene)<br />
A polyether monoamine containing ethylene oxide (EO) units <strong>and</strong> propylene<br />
oxide (PO) units is useful as a reactant with maleated poly(propylene)<br />
to form a reaction product that can be blended with poly(propylene). 146<br />
Generally, the polyether amines are made by aminating a polyol, such as<br />
a polyether polyol with ammonia in the presence of a catalyst such as the<br />
nickel-containing catalyst Ni/Cu/Cr.<br />
The mixing of the maleated poly(propylene) <strong>and</strong> polyetheramine<br />
may be carried out in a customary mixing apparatus including batch mixers,<br />
continuous mixers, kneaders, <strong>and</strong> extruders. For most applications,<br />
the preferred customary mixing apparatus is an extruder in which the polyetheramine<br />
is grafted onto the maleated poly(propylene). The residence<br />
time varies from about 25 to 300 seconds. The preferred temperature range<br />
is from about 190 to 260°C.<br />
Blends of poly(propylene), maleated poly(propylene), <strong>and</strong> Jeffamine<br />
M-2070 produced in an extruder exhibit the characteristics as shown<br />
in Table 16.4.<br />
Maleated poly(propylene) <strong>and</strong> polyether amine show improved<br />
paintability, improved impact resistance, <strong>and</strong> excellent mold flowability<br />
over blends of poly(propylene) <strong>and</strong> maleated poly(propylene).
572 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 16.4: Properties of Poly(propylene) Blends with Poly(propylene)<br />
Modified Polyether Amines 146<br />
Example 1 2 3 4 5 6<br />
% MAL-PP 20 20 20 30 30 30<br />
% M2070 0 2 4 0 2 4<br />
FM,[kpsi] 284 255 226 289 256 201<br />
StY, [psi] 8660 7980 7030 8750 7830 6170<br />
TE,% 8 16 10 4 13 5<br />
TSt [psi] 4990 4770 4280 5000 4630 3720<br />
NI [ft lb/in] 0.161 0.220 0.386 0.123 0.139 0.220<br />
UnI [ft lb/in] 12 14 10 10 14 5<br />
%MAL-PP % Maleated poly(propylene)<br />
% M2070 % Jeffamine 2070<br />
Rest filled with poly(propylene) to 100%<br />
FM Flexural modulus<br />
StY Stress at yield<br />
TE<br />
Tensile elongation<br />
TSt Tensile strength<br />
NI<br />
Notched Izod impact<br />
UnI Unnotched Izod impact<br />
16.5.3.3 Amidoamine Functions in Poly(propylene)<br />
Amidoamines can be obtained by reacting caprolactam, laurolactam or another<br />
cyclic lactam with a polyetheramine. The molar ratio of lactam to<br />
amine may vary in wide ranges. Water may be used to control the speed of<br />
the reaction <strong>and</strong> the molecular weight of the amidoamine product.<br />
The polyetheramines used to make the amidoamines are prepared<br />
from ethylene oxide <strong>and</strong> propylene oxide. Any combination of ethylene<br />
oxide <strong>and</strong> propylene oxide will work, however, the ratio of ethylene oxide<br />
to propylene oxide may be tailored to control the water absorption. The<br />
amount of ethylene oxide should be greater than about 90%. Maleated<br />
poly(propylene) is used for reaction of the amidoamines. 147<br />
The reaction takes place in an extruder in which the amidoamine reacts<br />
with the maleated poly(propylene) to form a reaction product at about<br />
240°C to about 260°C. Blends of poly(propylene), maleated poly(propylene),<br />
<strong>and</strong> amidoamine can be produced in a single-screw extruder.
Compatibilization 573<br />
16.5.4 Muconic Acid Grafted Polyolefin Compatibilizers<br />
Muconic acid is also known as 2,4-hexadienedioic acid. cis,cis-muconic<br />
acid <strong>and</strong> cis,trans-muconic acid are commercially available. Due to its<br />
double bonds <strong>and</strong> diacid functionality, muconic acid can undergo a wide<br />
variety of reactions. Many muconic acid derivatives are known, including<br />
lactones, sulfones, polyamides, polyesters, thioesters, addition polymers,<br />
<strong>and</strong> other compounds. Such compounds have a wide variety of uses, including<br />
use as surfactants, flame retardants, UV light stabilizers, thermoset<br />
plastics, thermoplastics, <strong>and</strong> coatings. Muconic acid units grafted onto a<br />
polyolefin backbone are compatibilizers. The muconic acid group itself<br />
may have special advantages in the reactive compatibilization of certain<br />
polymers due to its particular chemical properties compared to other functional<br />
groups. 148<br />
To manufacture the compatibilizer, the polyolefin is melt extruded<br />
with muconic acid at a temperature in the range of about 180°C to 220°C. A<br />
suitable initiator is Lupersol 130, an organic peroxide free-radical initiator<br />
containing 2,4-dimethyl-2,5-di(tert-butylperoxy)-3-hexyne. When the<br />
polyolefin <strong>and</strong> muconic acid are mixed <strong>and</strong> free radical addition is initiated<br />
a hydrogen atom on a polyolefin carbon atom (either on the main chain or<br />
on a side group) is replaced by a muconic acid side group; the muconic<br />
acid loses one of its double bonds as one of its carbon atoms bonds to the<br />
polyolefin carbon atom in place of the lost hydrogen <strong>and</strong> the muconic acid<br />
side group picks up another hydrogen atom. Only little polymer degradation<br />
during muconic acid grafting compared to the known degradation<br />
produced by grafting acrylic acid <strong>and</strong> other units onto polyolefins is observed.<br />
Muconic acid graft copolymers exhibit a greater intrinsic viscosity<br />
retention than acrylic acid graft copolymers. Muconic acid graft copolymers<br />
are also far more ductile.<br />
16.5.5 Polyfunctional <strong>Polymers</strong> <strong>and</strong> Modified Polyolefin<br />
By the reaction of a polyfunctional polymer with a modified polyolefin,<br />
crosslinked products may be formed. A copolymer of vinyloxazoline or<br />
2-isopropenyl-2-oxazoline (IPO) <strong>and</strong> styrene produced by Dow, containing<br />
ca. 1% oxazoline, has been used for the reaction with carboxylic acid<br />
functional polyolefins. 149, 150 A copolymer of styrene <strong>and</strong> 2-isopropenyl-<br />
2-oxazoline (SIPO) <strong>and</strong> a copolymer of ethylene <strong>and</strong> acrylic acid have been<br />
melt blended at 280°C in an extruder. 151
574 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
N<br />
C<br />
O<br />
CH 2<br />
CH 2<br />
+<br />
HO<br />
O<br />
C<br />
O<br />
C<br />
N<br />
H<br />
O<br />
CH 2 CH 2 O C<br />
Figure 16.4: Reaction of Oxazoline <strong>and</strong> Carboxylic Acid 152<br />
Other suitable polymers, being reactive with the oxazoline group,<br />
include those which contain amine, carboxylic acid, hydroxyl, epoxy, mercaptan,<br />
<strong>and</strong> anhydride in the polymer chain or as end groups. Examples<br />
are SIPO <strong>and</strong> a high density poly(ethylene)/maleic anhydride graft copolymer<br />
(HDPE/MA), a styrene/acrylonitrile/IPO terpolymer (SANIPO), <strong>and</strong><br />
a propylene/acrylic acid copolymer (PAA) with /6acrylic acid, 75% SIPO,<br />
<strong>and</strong> 25% of a carboxylated polyester resin, sold as Vitel VPE6434, SIPO<br />
<strong>and</strong> a vinylidene chloride/methacrylic acid copolymer with 1% methacrylic<br />
acid. 153 The reaction of the oxazoline group with a carboxylic acid group<br />
is shown in Figure 16.4.<br />
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117. M. G. Oliveira <strong>and</strong> B. G. Soares. Compatibilization of nitrile-butadiene rubber/ethylene-propylene-diene<br />
monomer blends by mercapto-modified ethylene-vinyl<br />
acetate copolymers. J. Appl. Polym. Sci., 91(3):1404–1412,<br />
February 2004.<br />
118. B. G. Soares, A. S. Sirqueira, M. G. Oliveira, <strong>and</strong> M. S. M. Almeida.<br />
The reactive compatibilization of EPDM-based elastomer blends. Kautsch.<br />
Gummi Kunstst., 55(9):454–459, September 2002.<br />
119. B. G. Soares, A. S. Sirqueira, M. G. Oliveira, <strong>and</strong> M. S. M. Almeida. Compatibilization<br />
of elastomer-based blends. Macromol. Symp., 189:45–58,<br />
November 2002.<br />
120. B. G. Soares. <strong>Reactive</strong> compatibilization of nitrile rubber/EPDM blends.<br />
Kautsch. Gummi Kunstst., 56(7-8):396–400, July–August 2003.<br />
121. R. Scaffalo, F. P. La Mantia, R. Bertani, <strong>and</strong> A. Sassi. Compatibilization of<br />
PA6/rubber blends by using an oxazoline functionalized rubber. Macromol.<br />
Symp., 202:67–76, September 2003.<br />
122. N. Moussaif, C. Pagnoulle, J. Riga, <strong>and</strong> R. Jerôme. XPS analysis of the<br />
PC/PVDF interface modified by PMMA. location of the PMMA at the interface.<br />
Polymer, 41(9):3391–3394, April 2000.
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123. G. S. Wildes, T. Harada, H. Keskkula, D. R. Paul, V. Janarthanan, <strong>and</strong> A. R.<br />
Padwa. Synthesis <strong>and</strong> characterization of an amine-functional SAN for the<br />
compatibilization of PC/ABS blends. Polymer, 40(11):3069–3082, May<br />
1999.<br />
124. S. Saikrasun, T. Amornsakchai, C. Sirisinha, W. Meesiri, <strong>and</strong> S. Bualek-<br />
Limcharoen. Kevlar reinforcement of polyolefin-based thermoplastic elastomer.<br />
Polymer, 40(23):6437–6442, November 1999.<br />
125. B. De Roover, J. Devaux, <strong>and</strong> R. Legras. PAmXD,6/PP-g-MA blends. I.<br />
compatibilization. J. Polym. Sci., Part A-1: Polym. Chem., 35:901–915,<br />
1997.<br />
126. B. De Roover, J. Devaux, <strong>and</strong> R. Legras. PAmXD,6/PP-g-MA blends. II.<br />
rheology <strong>and</strong> phase inversion location. J. Polym. Sci., Part A-1: Polym.<br />
Chem., 35:917–925, 1997.<br />
127. B. De Roover, J. Devaux, <strong>and</strong> R. Legras. PAmXD,6/PP-g-MA blends. III.<br />
microstructure, blend melt viscosity, <strong>and</strong> copolymer concentration relationship.<br />
J. Polym. Sci., Part A-1: Polym. Chem., 35:1313–1327, 1997.<br />
128. T. X. Xie <strong>and</strong> G. S. Yang. Effects of maleated styrene-(ethylene-co-butene)-<br />
styrene on compatibilization <strong>and</strong> properties of nylon-12,12/nylon6 blends.<br />
J. Appl. Polym. Sci., 93(3):1446–1453, August 2004.<br />
129. O. Okada, H. Keskkula, <strong>and</strong> D. R. Paul. Nylon 6 as a modifier for maleated<br />
ethylene-propylene elastomers. Polymer, 40(10):2699–2709, May 1999.<br />
130. S. G. Cottis <strong>and</strong> K. M. Natarajan. In situ compatibilization of PPE/polyethylene<br />
copolymer blends. US Patent 5 286 793, assigned to Istituto Guido<br />
Donegani (Milan, IT); Enichem America, Inc. (Monmouth Junction, NJ),<br />
February 15 1994.<br />
131. H. A. M. van Aert, G. J. M. van Steenpaal, L. Nelissen, P. J. Lemstra,<br />
J. Liska, <strong>and</strong> C. Bailly. <strong>Reactive</strong> compatibilization of blends of poly(2,6-dimethyl-1,4-phenylene<br />
ether) <strong>and</strong> poly(butylene terephthalate). Polymer,<br />
42(7):2803–2813, March 2001.<br />
132. K. Abe, S.-I. Yamauchi, <strong>and</strong> A. Ohkubo. Polyphenylene ether resin composition.<br />
US Patent 4 460 743, assigned to Mitsubishi Petrochemical Co., Ltd.<br />
(Tokyo, JP), July 17 1984.<br />
133. S. Togo, A. Amagai, Y. Kondo, <strong>and</strong> T. Yamada. Solvent-resistant polyphenylene<br />
ether resin composition. US Patent 4 914 153, assigned to Mitsubishi<br />
Gas Chemical Company, Inc. (Tokyo, JP), April 3 1990.<br />
134. C. K. Samios, K. G. Gravalos, <strong>and</strong> N. K. Kalfoglou. In situ compatibilization<br />
of polyurethane with poly(ethylene terephthalate). Eur. Polym. J.,<br />
36(5):937–947, May 2000.<br />
135. G. H. Hu <strong>and</strong> M. Lambla. Chemical reactions between immiscible polymers<br />
in the melt: Transesterification of poly(ethylene-co-methylacrylate) with<br />
mono-hydroxylated polystyrenes. J. Polym. Sci., Part A-1: Polym. Chem.,<br />
33(1):97–107, January 1995.
Compatibilization 585<br />
136. G.-H. Hu <strong>and</strong> M. Lambla. Catalysis <strong>and</strong> reactivity of the transesterification<br />
of ethylene <strong>and</strong> alkyl acrylate copolymers in solution <strong>and</strong> in the melt.<br />
Polymer, 35(14):3082–3090, July 1994.<br />
137. E. Rizzardo <strong>and</strong> G. Moad. Living radical polymerization. In J. C. Salamone,<br />
editor, The Polymeric Materials Encyclopaedia: Synthesis, Properties <strong>and</strong><br />
<strong>Applications</strong>, pages 795–797. CRC Press, Boca Raton, FL, 1999.<br />
138. B. J. C., D. Derouet, F. Epaillard, J. C. Soutif, G. Legeay, <strong>and</strong> K. Dušek. Hydroxyl-terminated<br />
polymers obtained by free-radical polymerization - synthesis,<br />
characterization, <strong>and</strong> applications. Adv. Polym. Sci., 81:167–223,<br />
1986.<br />
139. B. Ameduri, B. Boutevin, <strong>and</strong> P. Gramain. Synthesis of block copolymers<br />
by radical polymerization <strong>and</strong> telomerization. Adv. Polym. Sci., 127:87–142,<br />
1997.<br />
140. M. Melchiors, D. Margotte, H. Höcker, H. Keul, <strong>and</strong> A. Neumann. Process<br />
for the production of telechelic polymers, telechelic polymers produced in<br />
this manner <strong>and</strong> use thereof. US Patent 6 455 645, assigned to Bayer Aktiengesellschaft<br />
(Leverkusen, DE), September 24 2002.<br />
141. J. Wootthikanokkhan <strong>and</strong> B. Tongrubbai. Compatibilization efficacy of<br />
poly(isoprene-butyl acrylate) block copolymers in natural/acrylic rubber<br />
blends. J. Appl. Polym. Sci., 88(4):921–927, April 2003.<br />
142. M. F. Diaz, S. E. Barbosa, <strong>and</strong> N. J. Capiati. Polypropylene/polystyrene<br />
blends: In situ compatibilization by Friedel-Crafts alkylation reaction. J.<br />
Polym. Sci., Part. B: Polym. Phys., 42(3):452–462, February 2004.<br />
143. Y.-J. Sun, R. J. G. Willemse, T. M. Liu, <strong>and</strong> W. E. Baker. In situ compatibilization<br />
of polyolefin <strong>and</strong> polystyrene using Friedel-Crafts alkylation<br />
through reactive extrusion. Polymer, 39(11):2201–2208, 1998.<br />
144. Y. Gao, H. L. Huang, Z. H. Yao, D. Shi, Z. Ke, <strong>and</strong> J. H. Yin. Morphology,<br />
structure, <strong>and</strong> properties of in situ compatibilized linear low-density<br />
polyethylene/polystyrene <strong>and</strong> linear low-density polyethylene/high-impact<br />
polystyrene blends. J. Polym. Sci., Part. B: Polym. Phys., 41(15):<br />
1837–1849, August 2003.<br />
145. R. Mülhaupt, T. Duschek, <strong>and</strong> B. Rieger. Functional polypropylene blend<br />
compatibilizers. Macromol. Symp., 48-49:317–332, 1991.<br />
146. R. K. Evans, R. J. G. Dominguez, <strong>and</strong> C. R. J. Polyether monoamine with<br />
36-44 EO units <strong>and</strong> 1-6 PO units. US Patent 6 465 606, assigned to Huntsman<br />
Petrochemical Corporation (Austin, TX), October 15 2002.<br />
147. R. J. Clark. Amidoamine modification of polypropylene. US Patent<br />
5 668 217, assigned to Huntsman Petrochemical Corporation (Austin, TX),<br />
September 16 1997.<br />
148. P. N. Chen, Sr., M. M. Glick, M. M. Jaffe, <strong>and</strong> A. Forschirm. Muconic<br />
acid grafted polyolefin compatibilizers. US Patent 5 173 541, assigned to<br />
Hoechst Celanese Corp. (Somerville, DE), December 22 1997.
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149. W. E. Baker <strong>and</strong> M. Saleem. Coupling of reactive polystyrene <strong>and</strong> polyethylene<br />
in melts. Polymer, 28(12):2057–2062, November 1987.<br />
150. M. Saleem <strong>and</strong> W. E. Baker. In situ reactive compatibilization in polymer<br />
blends: Effects of functional group concentrations. J. Appl. Polym. Sci., 39:<br />
655–678, 1990.<br />
151. R. W. Hohlfeld. Polymer blends compatibilized with reactive polymers extended<br />
with miscible nonreactive polymers. US Patent 4 590 241, assigned<br />
to The Dow Chemical Company (Midl<strong>and</strong>, MI), May 20 1986.<br />
152. T. Vainio, G.-H. Hu, M. Lambla, <strong>and</strong> J. V. Seppala. Functionalized polypropylene<br />
prepared by melt free radical grafting of low volatile oxazoline<br />
<strong>and</strong> its potential in compatibilization of PP/PBT blends. J. Appl. Polym.<br />
Sci., 61(5):843–852, August 1996.<br />
153. J. E. Schuetz, R. W. Hohlfeld, <strong>and</strong> B. C. Meridith. Process for preparing<br />
compatibilized thermoplastic polymer blends <strong>and</strong> compositions thereof. US<br />
Patent 4 864 002, assigned to The Dow Chemical Company (Midl<strong>and</strong>, MI),<br />
September 5 1989.
17<br />
Rheology Control<br />
17.1 MELT FLOW RATE<br />
The technical terms melt flow index (MFI), melt flow rate (MFR), <strong>and</strong><br />
melt flow number (MFN) are used synonymously. Throughout the text we<br />
prefer to use melt flow rate.<br />
The melt flow rate is the measure of a polymer’s ability to flow under<br />
certain conditions. It measures a melt flow rate, which is the amount of<br />
polymer that flows over a period of time under specified conditions. Typical<br />
melt flow units of measurement are dg/min. Melt flow provides an<br />
indication of the resin’s processability, such as in extrusion or molding,<br />
where it is necessary to soften or melt the polymer. 1<br />
17.2 RHEOLOGY CONTROL TECHNIQUES<br />
High melt flow rate poly(propylene) can be produced directly in a polymerization<br />
reactor, but its production is often limited by the solubility of<br />
hydrogen in the reaction. Hydrogen is the most effective chain transfer<br />
agent for propylene polymerization reactions, whether the reaction takes<br />
place in solution or in the bulk monomer. 2<br />
Another method for producing high melt flow rate poly(propylene)<br />
is to degrade low melt flow rate poly(propylene) using controlled rheology.<br />
Controlled rheology treatments are often employed as alternative<br />
techniques for producing high melt flow rate poly(propylene) because these<br />
treatments do not depend on hydrogen solubility.<br />
587
588 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Controlled rheology treatments can also be used to increase production<br />
efficiency by converting the low melt flow rate polymers into high<br />
melt flow rate polymers without changing the reactors operating conditions.<br />
Thus, many manufacturers prefer controlled rheology treatments to<br />
produce high melt flow rate polymers.<br />
Poly(α-olefins), particularly poly(propylene), may have its weightaverage<br />
molecular weight decreased substantially, or its melt flow rate substantially<br />
increased, by controlled degradation of the polymer. This may<br />
be accomplished by<br />
1. Reaction of the polymer with free radicals or free radical-producing<br />
agents such as peroxides,<br />
2. Heat treatment, <strong>and</strong><br />
3. Subjecting the polymer to high shear, 3<br />
or combinations of these methods. The effect attained is that the polymer<br />
molecule scission occurs, resulting in an overall lowered molecular weight<br />
or elevated MFR.<br />
Early techniques have been developed to degrade <strong>and</strong> to narrow the<br />
molecular weight using high shear gradients at temperatures between the<br />
melting point <strong>and</strong> the temperature at which purely thermal degradation of<br />
the polyolefin occurs. 3<br />
The degradation of the polyolefin can be achieved by a metal salt<br />
catalyst. 4 A crystalline polyolefin is mixed with a metal salt of a carboxylic<br />
acid, <strong>and</strong> the resultant mixture is heated in an atmosphere which is<br />
substantially free of oxygen to a temperature of 275 to 450°C. Also an organic<br />
anhydride catalyst is suitable for degradation of polyolefins at 200 to<br />
400°C. 5 The controlled oxidative degradation of propylene polymers has<br />
been further proposed by injecting oxygen or an oxygen-containing gas<br />
<strong>and</strong> an organic or inorganic peroxide. Next the melt is subjected to a high<br />
shear. An essentially odor-free propylene polymer can be recovered with a<br />
melt flow rate higher than that of the feed polymer. 6<br />
The addition <strong>and</strong> reaction of a peroxide with polymer is well known<br />
in the industry <strong>and</strong> is known generally as vis-breaking or peroxide degradation.<br />
7 Polymer resins produced with a low melt flow may need to be further<br />
modified after their initial polymerization to improve their processability.<br />
This is typically done through controlled rheology (CR) techniques
Rheology Control 589<br />
wherein the molecular weight of the polymer is lowered, usually by the addition<br />
of peroxide, to improve its flowability. This secondary processing,<br />
however, adds additional processing steps <strong>and</strong> increases the cost of manufacturing.<br />
Controlled rheology processing may also degrade the polymer<br />
<strong>and</strong> leave peroxide residue so that its use may be limited in certain applications.<br />
17.2.1 Pelletizing<br />
While vis-breaking is useful to the finishing of the polymer, it creates a<br />
need for an extra process step <strong>and</strong> adds expense to the process in equipment<br />
<strong>and</strong> process requirements.<br />
Provision of vis-breaking or controlled rheology (CR) process initiators<br />
prior to or during pelletization is a complex operation.<br />
Typical pelletizing equipment operates at shear rates or temperatures<br />
sufficient to trigger molecular degradation. However, molecular degradation<br />
should not take place during pelletizing. Instead, it is desirable that<br />
vis-breaking is the last process step prior to the final polymer transformation<br />
into its desired product. If vis-breaking already occurs in a preprocess,<br />
the material would result in a low-viscosity, sticky mass rather than discreet<br />
easily to h<strong>and</strong>le pellets.<br />
This problem can be solved if the preparation of the pellets starts<br />
with a lower initial molecular weight polymer, or higher melt flow rate<br />
polymer. Such a material will generate less frictional heat in compounding<br />
into pellets. This means that the viscous dissipation of the heat will cause<br />
less peroxide activation <strong>and</strong> allow pelletizing at generally lower temperatures<br />
or at longer exposure periods.<br />
Using lower weight-average molecular weight M w , or higher melt<br />
flow rate, the starting material requires less of the vis-breaking agent, such<br />
as peroxide, to reach the desired very high or ultra-high melt flow rates.<br />
A further benefit is the formation of less of the undesirable by-products of<br />
peroxide degradation.<br />
Poly(propylene) with 30 to 33 g/min MFR <strong>and</strong> with xylene solubles<br />
of about 2 to 6% material is compounded with peroxides <strong>and</strong> 0.025% calcium<br />
stearate. To obtain a polymer with MFR in the range of 120 to 150<br />
g/min, about 1,800 to 2,000 ppm of peroxide will be added.<br />
The inclusion of other additives can be accomplished in a continuous<br />
blender in a separate step. The dry-blended material plus additive
590 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
is further compounded <strong>and</strong> pelletized under time <strong>and</strong> conditions where the<br />
peroxide would not react to decompose the polymer significantly. By keeping<br />
the residence time short <strong>and</strong> the temperature low to prevent significant<br />
molecular scission or degradation, the polymer can be neatly <strong>and</strong> cleanly<br />
pelletized. Thus, a useful, easily h<strong>and</strong>led, <strong>and</strong> convenient pelletized product<br />
is created. 7<br />
17.3 PEROXIDES FOR RHEOLOGY CONTROL<br />
The technique for controlling the rheology of homopolymers <strong>and</strong> copolymers<br />
of poly(propylene) consists of peroxide degradation of these polymers.<br />
It is used to develop fluid products in an efficient way without having<br />
a detrimental effect in terms of production flow rates by reducing the<br />
number of basic polymerization powders.<br />
It is also possible to melt a propylene homopolymer or copolymer<br />
powder <strong>and</strong> to incorporate in it a peroxide before the extrusion followed by<br />
granulation.<br />
Peroxide radicals can cause chain scission resulting in shorter polymer<br />
chains, which increases the melt flow rate of the polymer. Such modification<br />
also causes a decrease in the flexural modulus versus non-degraded<br />
polymer of similar final melt flow rate.<br />
The drawback of this process is the fact that these products have<br />
mechanical properties, strength <strong>and</strong> shock resistance that are weaker than<br />
those of a product that is obtained directly after polymerization, extrusion<br />
<strong>and</strong> granulation, or a powder that has been extruded <strong>and</strong> pelletized for a<br />
second time.<br />
Actually, a poly(propylene) resin that is degraded by a peroxide may<br />
contain peroxide radicals, thus runs the risk of modifying the viscosity of<br />
the resin when it is processed at elevated temperatures. During this transformation,<br />
the peroxide again degrades the resin to reduce its viscosity.<br />
Now, during storage, the peroxide has the tendency to migrate <strong>and</strong><br />
therefore to leave the resin. Thus, during the storage period, the resin may<br />
have a different behavior <strong>and</strong> show a viscosity that is different during or<br />
after processing, depending on whether there is a little or a lot of peroxide. 8<br />
17.3.1 Hydroperoxides<br />
Hydroperoxides for rheology control are shown in Table 17.1.
Rheology Control 591<br />
Table 17.1: Hydroperoxides for Controlled Rheology 8<br />
Hydroperoxide<br />
tert-Butyl hydroperoxide<br />
tert-Amyl hydroperoxide<br />
Pinane hydroperoxide<br />
Cumene hydroperoxide<br />
2,5-Dimethyl-2,5-di(hydroperoxy)hexane<br />
Diisopropylbenzene mono hydroperoxide<br />
Remarks<br />
Most common<br />
Common<br />
17.3.2 Peroxides<br />
Peroxides for rheology control are shown in Table 17.2.<br />
17.3.2.1 4-(tert-Amylperoxy)-4-methyl-2-pentanol<br />
4-(tert-Amylperoxy)-4-methyl-2-pentanol has over the years found utility<br />
as a reactant or a reaction catalyst which made use of its hydroxy functionality<br />
for various purposes. 9<br />
17.3.2.2 DHBP<br />
Over time, because of its safety in h<strong>and</strong>ling <strong>and</strong> decomposition temperature,<br />
one specific peroxide, 2,5-dimethyl-2,5-di(tert-butylperoxy)hexane<br />
(DHBP) also known as LUPEROX 101, Trigonox 101, <strong>and</strong> Interox,<br />
has become the industry st<strong>and</strong>ard for poly(propylene) modification. 9<br />
DHBP is a liquid, so the dosage <strong>and</strong> admixture are more comfortably<br />
compared to solid peroxides. Its half-life time is 5.9 s at 200°C. Typical<br />
decomposition side products of DHBP are considered to be acceptable for<br />
using it as an additive for food packages.<br />
17.3.2.3 Di-tert-butyl peroxide<br />
Di-tert-butyl peroxide (DTBP) has a particularly simple structure <strong>and</strong> from<br />
the commercial point of view is the most advantageous of these peroxides.<br />
However, it has high volatility <strong>and</strong> its use is therefore restricted. DTBP is<br />
only added in low concentrations, in the form of a master batch with a solid<br />
carrier. In addition, its ignition point is between 48 <strong>and</strong> 55°C, even under<br />
nitrogen. Safety issues in its use are therefore problematic. DTBP can be<br />
fed as a liquid via metering pumps to the extruder.
592 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Peroxide<br />
Table 17.2: Peroxides for Controlled Rheology 8<br />
Remarks<br />
Dibenzoyl peroxide<br />
p-Chlorobenzoyl peroxide<br />
Lauroyl peroxide (Dodecanoyl peroxide)<br />
Decanoyl peroxide<br />
3,5,5-Trimethylhexanoyl peroxide<br />
Acetyl peroxide<br />
2,5-Dimethyl-2,5-di(benzoylperoxy)hexane<br />
2,5-Dimethyl-2,5-di(2-ethylhexanoylperoxy)hexane<br />
2,2-Di(tert-butylperoxy)butane<br />
2,2-Di(tert-amyl)peroxypropane<br />
10<br />
4-(tert-Amylperoxy)-4-methyl-2-pentanol<br />
9<br />
1,1-Di(tert-butylperoxy)cyclohexane<br />
1,1-Di(tert-butylperoxy)-3,3,5-trimethylcyclohexane<br />
1,1-Di(tert-amylperoxy)cyclohexane<br />
2,2-Bis(4,4-di-tert-butylperoxycyclohexyl)propane<br />
2,5-Dimethyl-2,5-di(tert-butylperoxy)-3-hexyne Lupersol 130<br />
Di-tert-butyl peroxide<br />
Di-tert-amyl peroxide<br />
1,4-Di(tert-butylperoxyisopropyl)benzene<br />
2,5-Dimethyl-2,5-di(tert-butylperoxy)hexane Trigonox 101<br />
1,1,4,4,7,7-Hexamethylcyclo-4,7-diperoxynonane<br />
3,3,6,6,9,9-Hexamethylcyclo-1,2,4,5-tetraoxanonane<br />
3,6,6,9,9-Pentamethyl-3-n-propyl-1,2,4,5-tetraoxacyclononane<br />
10<br />
3,6,6,9,9-Pentamethyl-3-(ethyl acetate)-<br />
USP-138<br />
1,2,4,5-tetraoxacyclononane<br />
3-Phenyl-3-tert-butylperoxyphthalide
Rheology Control 593<br />
However, when the peroxide is added as a liquid to the extruder,<br />
disadvantages are often encountered in relation to polymer properties, in<br />
particular the film properties of degraded propylene polymers. There is<br />
the danger of explosion within the extruder. Gaseous DTBP is capable of<br />
exploding even in an inert gas atmosphere. If a gas explosion of this type<br />
extends to involve liquid peroxide, wherever it is present it can damage the<br />
extruder. 11<br />
Other compounds of this type which are more expensive but easier<br />
to h<strong>and</strong>le are frequently used in industrial applications.<br />
17.3.3 Diacyl Peroxides<br />
Diacyl peroxides <strong>and</strong> hydroperoxides often exhibit an induced decomposition.<br />
Acyl peroxides decompose into acyloxy radicals. These radicals<br />
undergo β-scission very fast to give the corresponding alkyl radical or aryl<br />
radical <strong>and</strong> eject carbon dioxide. Therefore, the acyloxy group is not observed<br />
in the decomposition products.<br />
17.3.4 Ketone Peroxides<br />
Methylethylketone peroxide <strong>and</strong> methylisobutylketone peroxide are known<br />
to be mixtures of several different ketone peroxide compounds, among<br />
which the noncyclic ketone peroxides predominate. However, these ketone<br />
peroxides do contain some small quantities of cyclic ketone peroxides<br />
which result from side reactions during the preparation of the methylethyl<br />
<strong>and</strong> methylisobutylketone peroxides. For example, in commercially available<br />
methylethylketone peroxides about 1 to 4% of the total active oxygen<br />
content is attributable to cyclic ketone peroxides.<br />
17.3.4.1 Cyclic Ketone Peroxides<br />
The cyclic ketone peroxides are exceptionally well suited for use in the<br />
modification of polymers. In general, the cyclic ketone peroxide trimers<br />
are less volatile <strong>and</strong> more reactive than the corresponding dimers.<br />
Cyclic peroxides can be made by reacting a ketone with hydrogen<br />
peroxide. Suitable ketones for use in the synthesis of the cyclic peroxides<br />
include methylethylketone, methylisobutylketone, diethylketone,<br />
<strong>and</strong> methylisopropylketone. Therefore, examples for cyclic peroxides are
594 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
H 3 C<br />
CH 3 CH 3<br />
CH 3 CH 3<br />
C O O C CH 2 CH 2 C O O C CH 3<br />
CH 3 CH 3 CH 3 CH 3<br />
2,5-Dimethyl-2,5-di(tert-butylperoxy)hexane<br />
H<br />
H 5 C 2<br />
CH 3<br />
O O<br />
C C C<br />
H 3 C C 2 H 5<br />
H 3 C<br />
O O<br />
2 5<br />
O<br />
C<br />
O<br />
3,6,9-Triethyl-3,6,9-trimethyl-1,4,7-triperoxonane<br />
Figure 17.1: 2,5-Dimethyl-2,5-di(tert-butylperoxy)hexane <strong>and</strong><br />
3,6,9-Triethyl-3,6,9-trimethyl-1,4,7-triperoxonane<br />
cyclic methylethylketone peroxide, cyclic methylisobutylketone peroxide,<br />
cyclic diethylketone peroxide, <strong>and</strong> cyclic methylisopropylketone peroxide.<br />
Cyclic ketone peroxides are composed of at least two ketone peroxide<br />
entities which may be the same or different. Thus, cyclic ketone peroxides<br />
may exist in the form of dimers, trimers, etc. When cyclic ketone<br />
peroxides are prepared, a mixture usually is formed which predominantly<br />
exists of the dimeric <strong>and</strong> trimeric forms. The ratio between the various<br />
forms mainly depends on the reaction conditions during the preparation.<br />
The peroxides can be prepared, transported, stored, <strong>and</strong> applied as<br />
such or in the form of powders, granules, pellets, pastilles, flakes, slabs,<br />
pastes, <strong>and</strong> solutions. These formulations may optionally be phlegmatized,<br />
as necessary, depending on the particular peroxide <strong>and</strong> its concentration in<br />
the formulation .<br />
Other examples for cyclic ketone peroxides, are, 12 e.g., 3,6,9-triethyl-3,6,9-trimethyl-1,4,7-triperoxonane,<br />
<strong>and</strong> 2,5-dimethyl-2,5-di(tert-butylperoxy)hexane,<br />
c.f. Figure 17.1. Cyclic ketone peroxides give a much<br />
higher degree of poly(propylene) degradation than their non-cyclic ketone<br />
peroxide counterparts. The degradation of polyolefins with cyclic ketone<br />
peroxides results in less yellowing than comparable processes employing<br />
their non-cyclic ketone peroxides. The principal advantage of these prod-
Rheology Control 595<br />
ucts is that they do not produce tert-butanol as a decomposition by-product.<br />
17.3.5 Masterbatches of Peroxides<br />
Masterbatching can be used to facilitate the process mixing the peroxide<br />
with the polyolefin. Masterbatching refers to a process of adding a small<br />
amount of poly(propylene), which has an organic peroxide <strong>and</strong>/or other<br />
additives within it, to a larger amount of poly(propylene) <strong>and</strong> subsequently<br />
blending <strong>and</strong> extruding in order to achieve the desired poly(propylene)<br />
characteristics.<br />
A problem in masterbatching is the melt blending of large amounts<br />
of peroxide into poly(propylene). This is difficult because the peroxide<br />
tends to decompose during the melt blending step. While some of the peroxide<br />
can survive the melt blending step, at least some degrades the poly-<br />
(propylene). Another problem with mixing solid poly(propylene) pellets,<br />
flakes, or powder with a liquid organic peroxide is that the poly(propylene)<br />
does not usually form a homogeneous, free-flowing phase with the liquid<br />
organic peroxide.<br />
Usually, an absorbent, such as silica, is added to the poly(propylene)<br />
in order to facilitate the addition of organic peroxide in the masterbatching<br />
process. However, an absorbent which is added to the poly(propylene) can<br />
interfere with the processing of the poly(propylene) material. Therefore,<br />
poly(propylene) which could absorb liquid organic peroxide without the<br />
necessity of using other absorbents, such as silica, is of great economic<br />
<strong>and</strong> scientific value.<br />
A free-flowing material typically contains 80 to 90% of poly(propylene)<br />
<strong>and</strong> 10 to 20% of liquid organic peroxide. The organic peroxide used<br />
can be any liquid organic peroxide, for example: 2,5-dimethyl-2,5-di(tertbutylperoxy)-3-hexyne,<br />
dicumylperoxide or 2,5-dimethyl-2,5-di-tert-butylperoxyhexane.<br />
13<br />
17.3.6 Peresters<br />
Peresters for controlled rheology are shown in Table 17.3. Peresters decompose<br />
into acyloxy <strong>and</strong> alkoxy radicals.<br />
17.3.7 Properties of Peroxides<br />
Peroxides used in industrial applications are shown in Table 17.4.
596 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 17.3: Peresters for Controlled Rheology 8<br />
Peresters<br />
tert-Butylperoxybenzoate<br />
tert-Butylperoxyacetate<br />
tert-Butylperoxy-3,5,5-trimethylhexanoate<br />
O,O-tert-Butyl-O-isopropyl monoperoxy carbonate<br />
O,O-tert-Butyl-O-(2-ethylhexyl)monoperoxy carbonate<br />
O,O-tert-Amyl-O-(2-ethylhexyl)monoperoxy carbonate<br />
tert-Butylperoxyisobutyrate<br />
tert-Butylperoxy-2-ethylhexanoate<br />
tert-Amylperoxy-2-ethylhexanoate<br />
tert-Butylperoxypivalate<br />
tert-Amylperoxypivalate<br />
tert-Butylperoxyneodecanoate<br />
tert-Butylperoxyisononanoate<br />
2,5-Dimethylhexene-2,5-diperoxyisononanoate<br />
tert-Amylperoxyneodecanoate<br />
α-Cumylperoxyneodecanoate<br />
3-Hydroxy-1,1-dimethylbutylperoxyneodecanoate<br />
tert-Butylperoxymaleate<br />
Ethyl-3,3-di(tert-butylperoxy)butyrate<br />
Ethyl-3,3-di(tert-amylperoxy)butyrate<br />
n-Butyl-4,4-di(tert-butylperoxy)valerate<br />
Di(2-ethylhexyl)peroxydicarbonate<br />
Dicyclohexylperoxydicarbonate
Rheology Control 597<br />
Table 17.4: Industrial Used Peroxides for Controlled Rheology <strong>and</strong> Crosslinking<br />
14<br />
Peroxide<br />
Remarks<br />
2,5-Dimethyl-2,5-di(tert-butylperoxy)- Lupersol 130,<br />
3-hexyne<br />
Mackine 201<br />
2,5-di(tert-Butylperoxy)hexyne<br />
DYBP<br />
Di(2-tert-butylperoxyisopropyl)benzene Perkadox 14-40<br />
Dicumyl hydroperoxide<br />
Perkadox BC-FF<br />
tert-Butyl hydroperoxide<br />
1,1-Di(tert-butylperoxy)-3,3,5-trimethylcyclohexane<br />
Varox 231-XL<br />
α,α ′ -Bis(tert-butylperoxy)diisopropyl benzene<br />
or crosslinking of<br />
Varox VC-R vulcanization<br />
elastomers<br />
Peroxide for Other Uses<br />
Remarks<br />
Dibenzoyl peroxide<br />
Curing<br />
MEK peroxide<br />
Curing<br />
Dicumyl peroxide<br />
Vulcanizing agent<br />
tert-Butylperoxybenzoate Esperox 10<br />
Lauroyl peroxide (Dodecanoyl peroxide)<br />
1,3-Di(2-tert-butylperoxyisopropyl)benzene<br />
Methylisobutylketone peroxide<br />
Methylethylketone peroxide<br />
Laurox W-25 Polymerization<br />
initiator<br />
Trigonox HM curing of unsaturated<br />
polyester resins<br />
Curing of unsaturated polyester<br />
resins
598 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
CH 3 CH 3<br />
C O O C<br />
CH 3 CH 3<br />
CH 3 CH 3<br />
C O* *O C<br />
CH 3 CH 3<br />
2<br />
O<br />
C<br />
CH 3<br />
*CH 3<br />
Figure 17.2: Decomposition of Dicumylperoxide 15<br />
Some peroxides suffer from excessively long half-lifes. However,<br />
the half-life of the initiator should be shorter than the residence time of<br />
the resin in the extruder. A long half-life is undesirable because it will<br />
lead to product quality problems due to residual peroxide in resin, or lower<br />
productivity or higher resin color depending on the amount of undecomposed<br />
peroxide in the resin. These include longer residence times or higher<br />
temperatures in the extruder. 9<br />
Often the use of safety diluent is required. Diluents are undesirable<br />
in at least some poly(propylene) grades because they may produce smoking<br />
or dripping in an end user’s extruder. It has been reported that diluents<br />
are also undesirable for fiber or film grades where, for example, they may<br />
adversely affect the feel of the surface.<br />
17.3.7.1 Mechanism of Decomposition<br />
Peroxides decompose in a rather complicated way in a multistep reaction.<br />
The mechanism of decomposition of dicumylperoxide is shown in Figure<br />
17.2. The mechanism of decomposition of dicumylperoxide is shown in<br />
Figure 17.3.
Rheology Control 599<br />
CH 3 CH 3 CH 3 CH 3<br />
CH 3 C O O C<br />
C O O C CH 3<br />
CH 3 CH 3 CH 3 CH 3<br />
4 * CH 3<br />
2 H 3 C<br />
O<br />
C<br />
CH 3<br />
O<br />
C<br />
O<br />
C<br />
CH 3<br />
CH 3<br />
Figure 17.3: Decomposition of 1,4-Di(tert-butylperoxyisopropyl)benzene 15<br />
17.3.7.2 Kinetics of Decomposition<br />
Most studies on the decomposition of peroxides have been done in dilute<br />
solutions at low temperatures at which only small concentrations of radicals<br />
occur at low pressures. The conditions under which grafting occurs in<br />
the extruder are different in these aspects:<br />
• High temperatures,<br />
• High pressures,<br />
• High viscous environment.<br />
For these reasons there is not much knowledge concerning the radical<br />
reaction in the extruder. However there are some qualitative statements.<br />
High temperatures decrease the selectivity of radical reactions. High pressures<br />
reduce the tendency of chain scission. In high viscous media, diffusion<br />
controlled reactions are significantly slower than in low viscous<br />
solutions.<br />
From kinetic constants it may be concluded that tert-alkoxy radicals<br />
favor the abstraction of hydrogen atoms rather than the addition on vinyl<br />
groups. This tendency is enhanced at higher temperatures.<br />
16, 17<br />
17.3.7.3 Half-life of Peroxides<br />
The half-life of peroxides listed is shown in Table 17.5. If the residence<br />
time is in the range of five half-life times, then the decomposition of the<br />
peroxide will reach more than 97%. If the half-life time is very short in
600 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 17.5: Half-life of Peroxides 10<br />
Peroxide °C a,b °C a,c<br />
LUPEROX 101 140 145<br />
2,2-Di(tert-amylperoxy)propane 128 –<br />
Di-tert-amyl peroxide 143 –<br />
MEK cyclic trimer – 158<br />
4-(tert-amylperoxy)-4-methyl-2-pentanol 141 –<br />
a One hour half-life time at the temperature specified<br />
b in dodecane<br />
c in poly(propylene)<br />
Table 17.6: Flash Points of Peroxides 10<br />
Peroxide Flash point [°C a ]<br />
LUPEROX 101 (92% assay) 49<br />
LUPEROX 101 (95% assay) 78<br />
Di-tert-amyl peroxide<br />
25 a<br />
4-(tert-Amylperoxy)-4-methyl-2-pentanol >60<br />
a Performed with ASTM D3278<br />
b Depending on preparation<br />
comparison to the residence time, then the peroxide decomposes to a great<br />
extent in the initial stage of the process. This results in high concentrations<br />
of radicals, <strong>and</strong> secondary radicals in the polymer backbone, which may<br />
result in an enhanced crosslinking.<br />
The majority of today’s production processes require that the peroxide<br />
be mixed with solid poly(propylene) in a blender. Under such conditions,<br />
it is crucial that the peroxide has a high flash point for safety. Flash<br />
points can be determined using the small scale closed cup method (ASTM<br />
D3278). Flash points of commercially available peroxides are shown in<br />
Table 17.6<br />
17.3.8 Azo Compounds<br />
Azo compounds are shown in Table 17.7. Azo compounds are advantageous<br />
over peroxides in that they show no or much less induced decomposition.<br />
However, the most common azonitriles, e.g., AIBN decompose too<br />
quickly at the required temperatures. In addition, the cyanoalkyl radicals
Rheology Control 601<br />
Table 17.7: Azo Compounds for Controlled Rheology 8<br />
Azo Compounds<br />
2,2 ′ -Azobis(2-acetoxy)propane<br />
2,2 ′ -Azobis(isobutyronitrile) (AIBN)<br />
2,2 ′ -Azobis(2,4-dimethylvaleronitrile)<br />
2,2 ′ -Azobis(cyclohexanenitrile)<br />
2,2 ′ -Azobis(2-methylbutyronitrile)<br />
2,2 ′ -Azobis(2,4-dimethyl-4-methoxyvaleronitrile)<br />
are comparatively unreactive to abstract hydrogen from a polyolefin.<br />
17.4 SCAVENGERS<br />
17.4.1 Stable Nitroxyl Radicals<br />
Incorporation of stable radicals that are always present after extrusion provides<br />
a better thermal stability to the products that are obtained, improves<br />
the UV resistance of the latter <strong>and</strong> reduces their tendency to depolymerize.<br />
In the case where a peroxide is also incorporated into the resin, the<br />
latter has a more stable viscosity over time because of comprising a reservoir<br />
of heat-reacting counter-radicals.<br />
However, the resin contains a reservoir of stable free radicals that<br />
have the tendency to neutralize the peroxide as soon as the latter is breaks<br />
down, thus reducing its degradation effects, regardless of whether its concentration<br />
is high or low. The storage time thus no longer has as much<br />
effect on the viscosity of the transformed resin. 8<br />
Stable nitroxyl radicals are shown in Table 17.8 <strong>and</strong> in Figure 17.4.<br />
The properties of stable nitroxyl radicals are described in the literature. 18<br />
17.5 MECHANISM OF DEGRADATION<br />
The degradation of poly(propylene) with peroxides is believed to occur via<br />
a series of free radical reactions involving steps such as initiation, scission,<br />
transfer <strong>and</strong> termination. The mechanism of degradation of a poly(propylene)<br />
by a peroxide is shown in Figure 17.5. First, the peroxide decomposes<br />
by a homolytic scission into two radicals. The tertiary carbon atom would<br />
yield most stable radicals <strong>and</strong> therefore is preferably attacked. The peroxide<br />
is deactivated by hydrogen transfer. In the next step, a scission of
602 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 17.8: Stable Nitroxyl Radicals for Controlled Rheology 8<br />
Nitroxyl Radicals<br />
2,2,5,5-Tetramethyl-1-pyrrolidinyloxy a<br />
3-Carboxy-2,2,5,5-tetramethyl-pyrrolidinyloxy b<br />
2,2,6,6-Tetramethyl-1-piperidinyloxy c<br />
4-Hydroxy-2,2,6,6-tetramethyl-1-piperidinyloxy d<br />
4-Methoxy-2,2,6,6-tetramethyl-1-piperidinyloxy e<br />
4-Oxo-2,2,6,6-tetramethyl-1-piperidinyloxy f<br />
Bis(1-oxyl-2,2,6,6-tetramethylpiperidine4-yl)sebacate g<br />
2,2,6,6-Tetramethyl-4-hydroxypiperidine-1-oxyl monophosphonate<br />
N-tert-Butyl-1-diethylphosphono-2,2-dimethylpropyl nitroxide h<br />
N-tert-Butyl-1-dibenzylphosphono-2,2-dimethylpropyl nitroxide<br />
N-tert-Butyl-1-di(2,2,2-trifluoroethyl)phosphono-2,2-dimethylpropyl nitroxide<br />
N-tert-Butyl[(1-diethylphosphono)-2-methyl-propyl]nitroxide<br />
N-(1-Methylethyl)-1-cyclohexyl-1-(diethylphosphono)nitroxide<br />
N-(1-Phenylbenzyl)-((1-diethylphosphono)-1-methyl ethyl)nitroxide<br />
N-Phenyl-1-diethylphosphono-2,2-dimethylpropyl nitroxide<br />
N-Phenyl-1-diethylphosphono-1-methyl ethyl nitroxide<br />
N-(1-Phenyl-2-methylpropyl)-1-diethylphosphono-1-methyl ethyl nitroxide<br />
N-tert-Butyl-1-phenyl-2-methylpropyl nitroxide<br />
N-tert-Butyl-1-(2-naphthyl)-2-methylpropyl nitroxide<br />
a PROXYL<br />
b 3-carboxy PROXYL<br />
c TEMPO<br />
d 4-hydroxy-TEMPO<br />
e 4-methoxy-TEMPO<br />
f<br />
4-oxo-TEMPO<br />
g CXA 5415<br />
h DEPN
Rheology Control 603<br />
H 3 C<br />
H 3 C<br />
N<br />
O -<br />
CH 3<br />
CH 3<br />
H 3 C<br />
H 3 C<br />
CH 3<br />
N<br />
CH<br />
O - 3<br />
PROXYL TM<br />
TEMPO TM<br />
H 3 C CH 3<br />
C H<br />
CH 3<br />
H 3 C C C CH 3<br />
P N<br />
H<br />
O CH<br />
2 C O 3<br />
O O -<br />
CH 3<br />
CH 2<br />
CH 3<br />
DEPN TM<br />
H 3 C<br />
H 3 C<br />
- O N<br />
H 3 C<br />
H 3 C<br />
O<br />
C<br />
O<br />
(CH 2 ) 3<br />
C<br />
O<br />
O<br />
CH 3<br />
CH 3<br />
N<br />
O -<br />
CH 3<br />
CH 3<br />
CXA 5415 TM<br />
Figure 17.4: Stable Nitroxyl Radicals: 2,2,5,5-Tetramethyl-1-pyrrolidinyloxy<br />
(PROXYL), 2,2,6,6-tetramethyl-1-piperidinyloxy (TEMPO), N-tert-butyl-1-diethylphosphono-2,2-dimethylpropyl<br />
nitroxide (DEPN), Bis(1-oxyl-2,2,6,6-tetramethylpiperidine4-yl)sebacate<br />
(CXA 5415)
604 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
R O O R R O* *O R<br />
R O*<br />
H H H<br />
CH 2 C CH 2 C CH 2 C<br />
CH 3 CH 3 CH 3<br />
R O H<br />
H<br />
H<br />
CH 2 C CH 2 C* CH 2 C<br />
CH 3 CH 3 CH 3<br />
H H<br />
CH 2 C CH 2 C*<br />
CH 3 CH 3<br />
CH 2<br />
C<br />
CH 3<br />
H H<br />
CH 2 C CH 2 C*<br />
CH 3 CH 3<br />
*C<br />
CH 3<br />
CH 2<br />
H H<br />
CH 2 C CH C H<br />
CH 3<br />
CH 3<br />
H<br />
C<br />
CH 3<br />
CH 2<br />
Figure 17.5: Mechanism of Degradation of a Poly(propylene) Chain
Rheology Control 605<br />
the main chain takes place. The radicals migrate to find another radical.<br />
Finally two radicals terminate by a disproportionation. A termination by<br />
recombination would be unfavorable in this case. In addition to the peroxide<br />
induced degradation, other models include the thermal decomposition<br />
of peroxides.<br />
17.6 ULTRA HIGH MELT FLOW POLY(PROPYLENE)<br />
Ultra high melt flow (UHMF) poly(propylene) generally has a melt flow<br />
of greater than about 30 g/min. The production of UHMF polymers can<br />
be achieved during their initial polymerization, without the need for secondary<br />
processing. This usually involves the addition of hydrogen during<br />
the polymerization reaction. Increasing the hydrogen concentration in the<br />
polymerization reactor, however, can result in the production of excessive<br />
xylene solubles, which is often undesirable. Equipment or process limitations<br />
may also limit the amount of hydrogen that can be used during the<br />
polymerization reaction. 1<br />
17.7 IRREGULAR FLOW IMPROVEMENT<br />
Molded parts made from typical controlled rheology-treated poly(propylene)<br />
tend to have inferior appearance <strong>and</strong> surface characteristics, <strong>and</strong> are<br />
often marred by flow marks such as tiger marks. Controlled rheology poly-<br />
(propylene) has a narrow molecular weight distribution which results from<br />
the selective loss of longer molecular chains due to the action of the organic<br />
peroxides. This narrow molecular weight distribution does not permit<br />
good surface molding of the molded article due to the irregular flow of<br />
the molten polymer in the mold. This irregular flow will lead to the surface<br />
flaws. Therefore, the use of controlled rheology poly(propylene) in<br />
injection molding has been limited to applications that do not require good<br />
surface characteristics.<br />
The addition of a high molecular weight component to the controlled<br />
rheology materials will improve the irregular flow in the mold. It is believed<br />
that this improvement occurs because of the broadened molecular<br />
weight distribution. However, the addition of the high molecular weight<br />
component sacrifices the high MFR properties gained in controlled rheology<br />
treatment.
606 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Thus, there is a need in the art for controlled rheology propylene<br />
polymers which have a high MFR <strong>and</strong> good surface characteristics when<br />
in injection molding.<br />
Poly(tetrafluoroethylene) (with a molecular weight above 1,000,000<br />
Dalton or even above about 5,000,000 Dalton) can be dispersed by mechanically<br />
blending with propylene polymers in the same extruder which<br />
is used for a simultaneous or subsequent controlled rheology treatment.<br />
Poly(tetrafluoroethylene) preferably can be dispersed simultaneously with<br />
the controlled rheology treatment in the extruder. A surface-modified poly-<br />
(tetrafluoroethylene) is particularly useful. This is an acrylic modified<br />
poly(tetrafluoroethylene), commercially available as Metablen. 2<br />
17.8 HETEROPHASIC COPOLYMERS<br />
Poly(propylene) heterophasic copolymers are typically made up of three<br />
components. These include a poly(propylene) homopolymer, a rubbery<br />
ethylene propylene copolymer, <strong>and</strong> a crystalline ethylene-rich ethylene<br />
propylene copolymer. The typical heterophasic morphology of these polymers<br />
consists of the rubbery ethylene propylene copolymer being dispersed<br />
as generally spherical domains within the semi-crystalline poly(propylene)<br />
homopolymer matrix.<br />
Poly(propylene) copolymers can be modified to improve their impact<br />
strength. This can be done through the use of elastomeric modifiers<br />
or with peroxides. When using elastomeric modifiers, the elastomeric<br />
modifiers are melt blended with the poly(propylene) copolymer,<br />
with the increased elastomer content typically contributing to a higher impact<br />
strength. Examples of elastomeric modifiers include ethylene/propylene<br />
rubber (EPR) <strong>and</strong> ethylene propylene diene monomer (EPDM) rubber.<br />
In poly(propylene) heterophasic copolymers modified with peroxides<br />
during the controlled rheology process, performance improvements<br />
can be achieved by adjusting the conditions under which the controlled<br />
rheology is carried out. By slowing deactivation of the peroxide, impact<br />
copolymers with higher impact strength <strong>and</strong> lower stiffness values can be<br />
attained, while achieving the desired final melt flow characteristics.<br />
A slower decomposition of the peroxide during controlled rheology<br />
polymer modification also slows down the vis-breaking reactions. This allows<br />
the polymer fluff to remain at a higher viscosity for longer periods of<br />
time during the extrusion. It is believed that by maintaining the polymer
Rheology Control 607<br />
viscosity at higher levels during extrusion, the rubber phase of the poly-<br />
(propylene) copolymer is more uniformly dispersed, which in turn results<br />
in higher impact strength for the same polymer modified with peroxide<br />
having shorter decomposition times.<br />
Linear peroxides having at least two peroxide groups, such as 2,5-dimethyl-2,5-di(tert-butylperoxy)hexane,<br />
are particularly suitable for delayed<br />
decomposition. Other suitable peroxides are the cyclic ketone peroxides,<br />
such as those disclosed in the literature, 12 e.g., 3,6,9-triethyl-3,6,9-trimethyl-1,4,7-triperoxonane,<br />
c.f. Figure 17.1.<br />
Improvements in impact strength for poly(propylene) heterophasic<br />
copolymers have been observed by slowing the decomposition or increasing<br />
the half-life of the peroxide during degradation. This is accomplished<br />
through a reduction in extrusion temperatures.<br />
Alternatively, a peroxide with a longer half-life than would otherwise<br />
be selected may also be employed if required by the extrusion conditions.<br />
Normal extrusion temperatures for most controlled rheology of<br />
heterophasic copolymers are usually from about 230°C to about 290°C.,<br />
but may be hotter depending upon the product being processed. By significantly<br />
reducing these temperatures, improvements in impact strength can<br />
be achieved.<br />
To achieve slower decomposition, the poly(propylene) heterophasic<br />
copolymer is extruded at temperatures sufficient to maintain the material<br />
in a molten state, but reduced from those used in conventional controlled<br />
rheology processes. Thus, extrusion temperatures may range anywhere<br />
from the minimum temperature to maintain the copolymer in a molten state<br />
up to about 215 °C. When such temperatures are employed, at least<br />
some amount of the peroxide will usually remain unconsumed within the<br />
extruded copolymer.<br />
In heterophasic poly(propylene) (PP), both the degradation <strong>and</strong> the<br />
functionalization mainly occur in the ethylene rich phase. A preferential<br />
attack of the free radicals at single tertiary hydrogens between ethylene<br />
units, or at the ends of a PP block adjacent to one or multiple ethylene<br />
units, results in a selective functionalization of the ethylene rich copolymers,<br />
regardless of the solubility parameter or decomposition rate of the<br />
peroxides.<br />
These tertiary hydrogen atoms are not sterically protected by adjacent<br />
methyl groups, <strong>and</strong> are therefore more accessible to the generated free<br />
radicals <strong>and</strong> the bulky maleic anhydride. 19
608 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
17.9 POLY(PROPYLENE)<br />
Commercial poly(propylene) resins commonly are polymerized by conventional<br />
Ziegler-Natta catalyst systems <strong>and</strong> have a high molecular weight<br />
<strong>and</strong> a broad molecular weight distribution (MWD). The chemical structure<br />
of poly(propylene) is generally influenced by the kind of polymerization<br />
system used during its production. Because the MWD largely determines<br />
the rheological properties of poly(propylene) melts, this parameter must<br />
be controlled to improve the material response during processing <strong>and</strong> to<br />
achieve the diversity in polymer grades suitable for the different applications<br />
of poly(propylene).<br />
Establishing of a broad molecular weight distribution of the poly-<br />
(propylene) in conventional reactors is difficult because it requires the addition<br />
of chain terminators <strong>and</strong> transfer agents. These operations decrease<br />
output of the reactor <strong>and</strong> are often uneconomical.<br />
The most important characteristic of peroxides is that the half-life<br />
time at 130°C must be higher than 1 hour <strong>and</strong> smaller than 10 hours. Examples<br />
of peroxides industrially accepted for this degradation reaction are<br />
given in Table 17.4.<br />
17.9.1 Long Chain Branched Poly(propylene)<br />
Poly(propylene) with long chain branches can be obtained by reactive extrusion<br />
of a poly(propylene) in the presence of a peroxide, a polyfunctional<br />
acrylate monomer <strong>and</strong> thiuram disulfide as co-reactant.<br />
The thiuram disulfide gives two dithiocarbamate radicals by thermal<br />
decomposition. These radicals react with the PP radicals in a reversible<br />
reaction. Therefore, a decrease in the instantaneous concentration of free<br />
radicals is achieved, which favors the branching reaction. In this way the<br />
β-scission is reduced. 20<br />
17.9.2 Effect of MFR on Temperature <strong>and</strong> Residence Time<br />
The initiator decomposition rate <strong>and</strong> residence time distribution in the extruder<br />
increase with increasing temperature. The change of the screw speed<br />
affects mixing <strong>and</strong> residence time distribution. So the MFR should increase<br />
with increasing residence time. However, if the process is performed at a<br />
sufficient long residence time to allow all degradation reactions to complete,<br />
a further increase in residence time will not change the MFR.
Rheology Control 609<br />
Is has been demonstrated with dicumyl peroxide (DCP) as radical<br />
generator, the melt flow rate increases with increasing amount of peroxide.<br />
Generally, the crystalline fraction of samples increases with increasing peroxide<br />
concentration. 14<br />
REFERENCES<br />
1. K. P. Blackmon, L. P. Barthel-Rosa, S. A. Malbari, D. J. Rauscher, <strong>and</strong> M. M.<br />
Daumerie. Production of ultra high melt flow polypropylene resins. US<br />
Patent 6 657 025, assigned to Fina Technology, Inc. (Houston, TX), December<br />
2 2003.<br />
2. M. Fujii <strong>and</strong> S. Kim. Polypropylene materials with high melt flow rate <strong>and</strong><br />
good molding characteristics <strong>and</strong> methods of making. US Patent 6 599 985,<br />
assigned to Sunoco Inc. (R&M) (Philadelphia, PA), July 29 2003.<br />
3. G. Schmidtthomee, C. Alt, R. Herbeck, H. Moeller, <strong>and</strong> H. G. Trieschmann.<br />
Narrowing the molecular weight distribution of polyolefins. GB Patent<br />
1 042 178, assigned to BASF AG, September 14 1966.<br />
4. J. J. Baron, Jr. <strong>and</strong> J. P. Rakus. Thermal degradation of polyolefins in the<br />
presence of a metal salt carboxylic acid catalyst. US Patent 3 332 926, assigned<br />
to Allied Chem, July 25 1967.<br />
5. R. L. McConnell <strong>and</strong> D. A. Weemes. Method for making polyolefin waxes by<br />
thermal degradation of higher molecular weight polyolefins in the presence<br />
of organic acids <strong>and</strong> anhydrides. US Patent 3 519 609, assigned to Eastman<br />
Kodak Co, July 7 1970.<br />
6. E. G. Castagna, A. Schrage, <strong>and</strong> M. Repiscak. Process for controlled degradation<br />
of propylene polymers. US Patent 3 940 379, assigned to Dart Industries,<br />
Inc. (Los Angeles, CA), February 24 1976.<br />
7. M. W. Musgrave. Pelletized polyolefin having ultra-high melt flow <strong>and</strong> its<br />
articles of manufacture. US Patent 6 423 800, assigned to Fina Technology,<br />
Inc. (Houston, TX), July 23 2002.<br />
8. D. Bertin <strong>and</strong> P. Robert. Method for the production of a controlled rheological<br />
polypropylene resin. US Patent 6 620 892, assigned to Atofina (Puteaux, FR),<br />
September 16 2003.<br />
9. L. Kasehagen, R. Kazmierczak, R. Cordova, <strong>and</strong> T. Myers. Safe, efficient,<br />
low t-butanol forming organic peroxide for polypropylene modification. US<br />
Patent 6 599 990, assigned to Atofina Chemicals, Inc. (Philadelphia, PA), July<br />
29 2003.<br />
10. R. J. Ehrig <strong>and</strong> R. C. Weil. Controlled-rheology polypropylene. US<br />
Patent 4 707 524, assigned to Aristech Chemical Corporation (Pittsburgh,<br />
PA), November 17 1987.
610 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
11. K. Huber, J. Schwind, K. Lehr, H. Elser, H. Klassen, <strong>and</strong> K.-H. Kagerbauer.<br />
Peroxidic treatment of olefin polymers. US Patent 6 313 228, assigned to<br />
Basell Polyolefine GmbH (Ludwigshafen, DE), November 6 2001.<br />
12. J. Meijer, A. H. Hogt, G. Bekendam, <strong>and</strong> L. A. Stigter. Modification of (co)<br />
polymers with cyclic ketone peroxides. US Patent 5 932 660, assigned to<br />
Akzo Nobel NV (Arnhem, NL), August 3 1999.<br />
13. J. D. Adams, R. H. Dorn, M. J. King, J. L. Kulasa, N. J. Motto, L. J.<br />
Ostanek, <strong>and</strong> D. Petticord. High organic peroxide content polypropylene.<br />
US Patent 5 198 506, assigned to Phillips Petroleum Company (Bartlesville,<br />
OK), March 30 1993.<br />
14. H. Azizi <strong>and</strong> I. Ghasemi. <strong>Reactive</strong> extrusion of polypropylene: production<br />
of controlled-rheology polypropylene (CRPP) by peroxide-promoted degradation.<br />
Polymer Testing, 23(2):137–143, April 2004.<br />
15. T. Bremner <strong>and</strong> A. Rudin. Peroxide modification of linear low density polyethylene:<br />
A comparison of dialkyl peroxides. J. Appl. Polym. Sci., 49:<br />
785–798, 1993.<br />
16. G. Moad. The synthesis of polyolefin graft copolymers by reactive extrusion.<br />
Prog. Polym. Sci., 24(1):81–142, April 1999.<br />
17. G. Moad. Corrigendum to “the synthesis of polyolefin graft copolymers<br />
by reactive extrusion”[progress in polymer science 1999;24:81-142]. Prog.<br />
Polym. Sci., 24(10):1527–1528, December 1999.<br />
18. L. B. Volodarsky, V. A. Reznikov, <strong>and</strong> V. I. Ovcharenko. Synthetic Chemistry<br />
of Stable Nitroxides. CRC Press, Boca Raton, FL, 1994.<br />
19. T. Kamfjord <strong>and</strong> A. Stori. Selective functionalization of the ethylene rich<br />
phase of a heterophasic polypropylene. Polymer, 42(7):2767–2775, March<br />
2001.<br />
20. D. Graebling. Synthesis of branched polypropylene by a reactive extrusion<br />
process. Macromolecules, 35(12):4602–4610, June 2002.
18<br />
Grafting<br />
Pros <strong>and</strong> cons of grafting copolymers by reactive extrusion in comparison<br />
to other methods are: 1, 2<br />
+ essentially no solvents,<br />
− intimate mixing of reactants compulsory,<br />
− the high reaction temperatures needed,<br />
+ fast preparation,<br />
− side reactions, e.g., degradation, crosslinking or discoloration,<br />
+ simple product isolation,<br />
+ extrusion is a continuous process.<br />
Grafting takes place mostly by a radical reaction mechanism 3 <strong>and</strong> is<br />
also called free radical grafting. However, there are other techniques for introducing<br />
functional groups into polymers, e.g., according to the Alder-ene<br />
reaction. 4<br />
18.1 THE TECHNIQUES IN GRAFTING<br />
18.1.1 Parameters that Influence Grafting<br />
18.1.1.1 Mixing<br />
Efficient mixing of the individual components is of critical importance for<br />
the success of a graft process. The mixing efficiency is dependent on the<br />
screw geometry, the melt temperature, the pressure, the rheological prop-<br />
611
612 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
erties of the polymer, <strong>and</strong> the solubilities of the monomer <strong>and</strong> the initiator,<br />
respectively, in the polyolefin.<br />
18.1.1.2 Grafting Efficiency<br />
In order to obtain a high grafting efficiency together with an effective suppression<br />
of the side reactions, it is necessary to transform the macroradicals<br />
on the backbone as far as possible into graft sites. In general, within<br />
reasonable limits, higher reaction temperatures, higher initiator levels, <strong>and</strong><br />
lower throughput rates result in higher grafting efficiency.<br />
Peroxide Concentration. The grafting efficiency of maleic anhydride on<br />
low density poly(ethylene) (LDPE) increases as the concentration of the<br />
peroxide increases. Further, the grafting efficiency depends on the means<br />
of reactive processing. In a comparative study with varying experimental<br />
setup, the lowest efficiency was found for extrusion using a typical shaping<br />
extrusion head, a higher efficiency was found with a static mixer <strong>and</strong> the<br />
highest efficiency was found with a dynamic mixer. The dynamic mixer<br />
is a cavity transfer mixer that provides shear rates of the moving melt of<br />
about 100 s −1 .<br />
Propene Content. In a series of polyolefins with different ethene/propene,<br />
the efficiency of grafting of maleic anhydride (MA) both in the melt<br />
<strong>and</strong> in solution was studied. The maleic anhydride graft content is low for<br />
polyolefins with high propene content, increases as the propene content decreases,<br />
<strong>and</strong> reaches a plateau at propene levels below 50%. Branching <strong>and</strong><br />
crosslinking occurs for polyolefins with low propene content, while degradation<br />
is the main side reaction for polyolefins with high propene content. 5<br />
Mechanochemistry. Shear stresses in the dynamic mixer cause a formation<br />
of radicals even in the absence of any peroxide. Therefore, grafting<br />
of maleic anhydride on LDPE even without the action of peroxide initiator<br />
is observed. The dynamic mixer helps to obtain a high grafting efficiency<br />
on LDPE using a small concentration of peroxide initiator. Under these<br />
conditions, grafting is not accompanied by a crosslinking reaction of the<br />
poly(ethylene) chains. 6
Grafting 613<br />
18.1.1.3 Screw Geometry<br />
<strong>Reactive</strong> extruders usually have a modular construction. This allows flexible<br />
arrangements of the screw elements <strong>and</strong> barrel sections as needed.<br />
18.1.1.4 Processing Temperature<br />
The processing temperature is of critical importance. Too high processing<br />
temperatures will cause degradation reaction, <strong>and</strong> the initiator may decompose<br />
too quickly to be effective.<br />
18.1.1.5 Processing Pressure<br />
In contrast to temperature, a high processing pressure can improve the solubility<br />
of the monomer to be grafted <strong>and</strong> the solubility of the initiator in<br />
the polymer.<br />
18.1.1.6 Residence Time<br />
The residence time is governed by the overall throughput which can be<br />
adjusted by the screw speed, the screw design, <strong>and</strong> the geometry of the<br />
extruder.<br />
18.1.1.7 Removal of By-Products<br />
The unreacted monomers <strong>and</strong> decomposition products from the initiator,<br />
etc., are removed by the application of vacuum to the melt.<br />
18.1.1.8 Consistency<br />
Experiments of grafting maleic anhydride onto poly(propylene) by melt<br />
extrusion with dicumyl peroxide, where the poly(propylene) was fed either<br />
as powder or in granular form, showed that consistency plays a role<br />
on the degree of grafting. 7 The grafting efficiency of powdered poly(propylene)<br />
was higher than that obtained for the granular form of poly(propylene).<br />
It is believed that the grafting of powder is more successful because<br />
a better initial mixing <strong>and</strong> less diffusional resistance during the grafting is<br />
provided.
614 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 18.1: Reaction Temperatures for Coupling of Stable Radicals 8<br />
Polymer Abbreviation Temperature [°C]<br />
Low density poly(ethylene) LDPE 170–260<br />
High density poly(ethylene) HDPE 180–270<br />
Poly(propylene) PP 180–280<br />
Poly(styrene) PS 190–280<br />
Styrene-block copolymers SB(S) 180–260<br />
Ethylene-propylene-diene modified EPDM 180–260<br />
Ethylene/propylene rubber EPR 180–260<br />
18.1.2 Free Radical Induced Grafting<br />
The most commonly used grafting method is free radical induced grafting.<br />
However, the efficiency of grafting cannot simply be increased by increasing<br />
only the concentration of the radical initiator. More important for the<br />
grafting efficiency are proper mixing <strong>and</strong> a sophisticated choice of proper<br />
comonomers.<br />
Grafting without radical initiator is also possible. In this case, the<br />
macroradicals are formed by a shear induced chain scission. Of course,<br />
this process is accompanied by degradation or crosslinking reactions.<br />
18.1.3 Grafting Using Stable Radicals<br />
The technique of grafting using stable radicals involves two steps. 8<br />
1. A stable nitroxyl radical is grafted onto a polymer, which involves<br />
the heating of a polymer <strong>and</strong> a stable nitroxyl radical.<br />
2. The grafted polymer of the first step is then heated in the presence<br />
of a vinyl monomer or oligomer to a temperature at which cleavage<br />
of the nitroxyl-polymer bond occurs <strong>and</strong> polymerization of the<br />
vinyl monomer is initiated at the polymer radical.<br />
The temperature applied in the first reaction step depends on the<br />
polymer <strong>and</strong> is for example, 50°C to 150°C above the glass transition temperature<br />
(T g ) for amorphous polymers <strong>and</strong> 20°C to 180°C above the melting<br />
temperature (T m ) for semi-crystalline polymers. Typical temperatures<br />
are summarized in Table 18.1.<br />
Stable nitroxyl radicals are collected in Table 18.2. The first step of<br />
the process is performed conveniently in an extruder or a kneading appa-
Compound<br />
Table 18.2: Stable Nitroxyl Radicals<br />
Grafting 615<br />
Benzoic acid 2,2,6,6-tetramethyl-piperidin-1-oxyl-4-yl ester<br />
4-Hydroxy-2,2,6,6-tetramethyl-piperidin-1-oxyl<br />
4-Propoxy-2,2,6,6-tetramethyl-piperidin-1-oxyl<br />
Decanedioic acid bis(2,2,6,6-tetramethyl-piperidin-1-oxyl-4-yl)<br />
ratus. In the extruder, a reduced pressure of less than 200 mbar is applied<br />
during extrusion. Volatile by-products may be removed thereby. Typical<br />
reaction times are from 2 min to 20 min.<br />
For the monomer grafting reactions, unsaturated monomers are selected<br />
from styrene, dodecyl acrylate, <strong>and</strong> other compounds. The second<br />
reaction step may be performed immediately after the first step, however it<br />
is also possible to store the intermediate polymeric radical initiator at room<br />
temperature for some time.<br />
Because the graft polymerization is a living polymerization, it can be<br />
started <strong>and</strong> stopped practically at will. The intermediate polymeric radical<br />
initiator is stable at room temperature <strong>and</strong> no loss of activity occurs up to<br />
several months.<br />
The reaction step may also be performed in a mixer or extruder.<br />
However, it is also possible to dissolve or disperse the polymer <strong>and</strong> to add<br />
the monomer to the solution. If the second reaction step is performed in a<br />
melt, a reaction time of 2 to 20 min is adequate.<br />
The grafted polymers are useful in many applications such as compatibilizers<br />
in polymer blends or alloys, adhesion promoters between two<br />
different substrates, surface modification agents, nucleating agents, coupling<br />
agents between filler <strong>and</strong> polymer matrix, or dispersing agents. The<br />
process is particularly useful for the preparation of grafted block copolymers.<br />
Grafted block copolymers of poly(styrene) <strong>and</strong> polyacrylate are useful<br />
as adhesives or as compatibilizers for polymer blends or as polymer<br />
toughening agents. Poly(methyl methacrylate-co-acrylate) diblock graft<br />
copolymers or poly(methyl acrylate-co-acrylate-co-methacrylate) triblock<br />
graft copolymers are useful as dispersing agents for coating systems, as<br />
coating additives or as resin components in coatings. Graft block copolymers<br />
of styrene, (meth)acrylates, or acrylonitrile are useful for plastics,<br />
elastomers, <strong>and</strong> adhesives.
616 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 18.3: Monomers for grafting onto Polyolefins 1<br />
Vinyl Monomer<br />
Remarks/References<br />
Maleic anhydride<br />
Most common<br />
Maleate esters<br />
9<br />
Styrene Auxiliary monomer 10<br />
Maleimide derivatives<br />
11<br />
Methacrylate esters<br />
12<br />
Acetoacetoxy methyl methacrylate<br />
11<br />
Glycidyl methacrylate<br />
13, 14<br />
Acrylate esters<br />
15<br />
Ricinoloxazoline maleate<br />
16<br />
Vinylsilanes<br />
17<br />
18.2 POLYOLEFINS<br />
The synthesis of polyolefin graft copolymers by reactive extrusion has been<br />
reviewed by Moad. 1, 2 The methods of modification can be classified as<br />
1. Free radical induced grafting of unsaturated monomers onto polyolefins,<br />
2. End-functional polyolefins by the ‘ene’ reaction,<br />
3. Hydrosilylation,<br />
4. Carbene insertion, <strong>and</strong><br />
5. Transformation of pending functional groups on polyolefins, e.g.,<br />
by transesterification, alcoholysis.<br />
18.2.1 Monomers for Grafting onto Polyolefins<br />
Monomers for grafting onto polyolefins are listed in Table 18.3.<br />
18.2.1.1 Macromonomers<br />
Polymeric or oligomeric vinyl compounds are addressed as macromonomers<br />
in the field of reactive extrusion. Examples for macromonomers<br />
are higher molecular acrylate esters, methacrylate esters, <strong>and</strong> maleimides.<br />
Macromonomers are less likely to undergo homopolymerization than low<br />
molecular vinyl compounds. This property arises due to steric effects.<br />
Thus they may not form longer pendent chains on the grafting sites consisting<br />
of homopolymers. A disadvantage of macromonomers is their low
Grafting 617<br />
HC CH<br />
O C C O<br />
OH OH<br />
CH 3<br />
C O<br />
CH 3 O<br />
C CH<br />
C C O<br />
OH OH<br />
CH 3<br />
C O C 6 H 12 CH<br />
CH 3 O<br />
C CH 2<br />
C C O<br />
OH OH<br />
Figure 18.1: Structure of Low Molecular Weight Fraction of Extrudates of Poly-<br />
(propylene) with Maleic anhydride <strong>and</strong> Dicumyl peroxide<br />
volatility. For this reason, an unreacted or excess compound may not easily<br />
be removed by vacuum treatment in the extrusion device.<br />
18.2.2 Mechanism of Melt Grafting<br />
Functionalized poly(propylene) (PP) has been used extensively for compatibilization<br />
of immiscible poly(propylene)/polyamide <strong>and</strong> poly(propylene)/polyester<br />
blends. Also, the interfacial adhesion of PP with glass <strong>and</strong><br />
carbon fibers can be improved. Further, functionalized PP is a processing<br />
aid for degradable plastics.<br />
18, 19<br />
It is generally accepted that chain scission occurs during the peroxide<br />
initiated functionalization of PP. 20 Maleic anhydride (MA) is appended<br />
to a tertiary carbon atom along the PP backbone as a single ring or as a<br />
short pendant chain due to the homopolymerization of MA. 21 On the other<br />
h<strong>and</strong>, according to the ceiling temperature, there is no possibility for the<br />
homopolymerization of MA under the melt grafting process conditions at<br />
190°C. 22<br />
Chemical analysis of the low molecular weight fraction of extrudates<br />
of poly(propylene) with maleic anhydride <strong>and</strong> dicumyl peroxide by<br />
mass spectrometry indicated the products shown in Figure 18.1. No MA<br />
oligomers or MA homopolymers are found in the low molecular weight<br />
fraction. The MA radicals always contain double bonds after termination.<br />
Peroxide residues are attached to MA molecules. A reduction of the<br />
molecular weight occurs when the degree of grafting increases. From the
618 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
inspection of the chemical structure of the low molecular weight residue, it<br />
can be concluded that the maleic anhydride is attached as a single moiety<br />
on the tertiary carbon atoms of the poly(propylene) backbone. From these<br />
experimental findings a mechanism of grafting has been proposed 23 that is<br />
given in Figure 18.2. Furthermore, the grafting of maleic anhydride onto<br />
poly(propylene) has been studied by a Monte Carlo simulation method. 24<br />
The results presented in this study are in agreement with the experiments.<br />
The grafting efficiency of methyl methacrylate is similar to that of maleic<br />
anhydride. 12<br />
18.2.3 Side Reactions<br />
Side reactions accompany the grafting reaction of polyolefins. These include<br />
1, 2<br />
1. Radical induced crosslinking of the polyolefin substrate,<br />
2. Radical induced chain scission of the polyolefin substrate,<br />
3. Shear induced degradation of the polyolefin substrate,<br />
4. Homopolymerization of the monomer, <strong>and</strong><br />
5. Side reactions which lead to a coloration of the product.<br />
The extent of the side reactions depends on the type of polyolefin.<br />
Some poly(ethylene) types are sensitive to branching <strong>and</strong> crosslinking.<br />
This is due to the recombination of the macroradicals. 25<br />
Poly(propylene) <strong>and</strong> linear low density poly(ethylene) copolymers<br />
undergo degradation rather than crosslinking, although crosslinking may<br />
occur. Degradation is often favored to synthesize controlled rheology<br />
types.<br />
18.2.4 Viscosity<br />
The formation of products with higher molecular weight is indicated by an<br />
increase of the apparent viscosity. On the other h<strong>and</strong>, by the introduction<br />
of polar groups during grafting, an increase of the viscosity is observed<br />
because of physical crosslinks of the individual molecules.<br />
Maleic anhydride has been grafted onto poly(propylene) in the presence<br />
of supercritical carbon dioxide. Supercritical carbon dioxide was used<br />
in order to reduce the viscosity of the poly(propylene) melt phase. A reduced<br />
viscosity should promote a better mixing of the reactants. The characterization<br />
of the products showed that the use of supercritical carbon
Grafting 619<br />
O<br />
O<br />
O<br />
CH 3 CH 3 CH 3 CH 3 CH 3<br />
CH 3 CH 3 CH 3 CH 3 CH 3<br />
CH 3 CH 3 CH 3 CH 3 CH 3<br />
O<br />
O<br />
O<br />
CH 3 CH 3 CH 3 CH 3 CH 3<br />
Figure 18.2: Mechanism of Grafting of Maleic anhydride onto Poly(propylene) 23<br />
(abbreviated)
620 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 18.4: Ceiling Temperatures for Important Monomers in <strong>Reactive</strong><br />
Extrusion Grafting1, 26<br />
Monomer<br />
Ceiling Temperature [°C]<br />
Maleic anhydride 400<br />
Methacrylate esters<br />
∼200<br />
Acrylate esters >400<br />
dioxide in fact resulted in improved grafting when high levels of maleic<br />
anhydride were used. No evidence of an improvement in the homogeneity<br />
of the product was observed. However, melt flow rate showed a reduction<br />
in the degradation of poly(propylene) during the grafting reaction when<br />
low levels of maleic anhydride were used. 27<br />
18.2.5 Ceiling Temperature<br />
The ceiling temperature is an important parameter for the ability of polymerization<br />
itself. We are dealing here with homopolymerization. The<br />
concept of the ceiling temperature is not restricted to a polymerization<br />
mechanism, because it deals with the thermodynamic equilibrium. Ceiling<br />
temperatures for important monomers in reactive extrusion grafting onto<br />
polyolefins are given in Table 18.4.<br />
The ceiling temperatures given in Table 18.4 could be important for<br />
the grafting of maleic anhydride <strong>and</strong> maleic esters.<br />
28, 29<br />
The ceiling temperatures depend on the pressure <strong>and</strong> on the concentration<br />
of the monomer. They are usually calculated from the heats <strong>and</strong><br />
the entropies of polymerization that are usually given at one atmosphere.<br />
In fact, the homopolymerization of maleic anhydride was observed at a<br />
higher temperature than 150°C, even when the ceiling temperature would<br />
not predict a polymerization reaction.<br />
18.2.6 Effect of Initiator Solubility<br />
Experiments of grafting of itaconic acid (IA) onto a low density poly(ethylene)<br />
(LDPE) with various initiators in the course of the reactive extrusion<br />
revealed that the solubility of the peroxide initiator in the molten polymer<br />
is the most important parameter in the IA grafting onto LDPE. The kinetics<br />
of decomposition is an important parameter for the efficiency of grafting.
Peroxide<br />
Table 18.5: Solubility Parameters of Peroxides 30<br />
Grafting 621<br />
δ [Jcm −3 ] 1/2 a<br />
Dicumyl peroxide 17.4<br />
2,5-Dimethyl-2,5-di(tert-butylperoxy)hexane 11.3<br />
Di-tert-butyl peroxide 15.3<br />
2,2-Di(tert-butylperoxy)-5,5,6-trimethyl bicyclo[2.2.1]heptane 16.1<br />
2,5-Dimethyl-2,5-di(tert-butylperoxy)-3-hexyne 19.1<br />
a calculated for 25°C<br />
The solubility parameters of various peroxides are collected in Table 18.5.<br />
The solubility parameters δ in Table 18.5 are calculated from group contributions<br />
31 according to Eq. 18.1.<br />
√<br />
∑<br />
δ = i ∆E i<br />
(18.1)<br />
N a ∑ i ∆V i<br />
∆E i Contribution of every atom <strong>and</strong> type of the intermolecular interaction<br />
in the molar cohesion energy<br />
∆V i van der Waals volume of a group constituting the molecule<br />
N a Avogadro number<br />
The temperature dependence of δ can be expressed by Eq. 18.2:<br />
logδ(T) = logδ(298K) − αk(T − 298) (18.2)<br />
k is a coefficient. For the polyolefin k = 1 <strong>and</strong> for the peroxides <strong>and</strong><br />
the monomer k = 1.25. α is the linear thermal expansion coefficient. The<br />
cohesion energy density δ calculated from Eq. 18.1 correlates well with the<br />
values obtained from the heat of vaporization of the respective substances.<br />
Substances are thermodynamically miscible in the absence of strong<br />
specific interactions between them, if their solubility parameters differ by<br />
less than 2 (Jcm −3 ) 1/2 . The solubility parameters of IA <strong>and</strong> LDPE are 24.6<br />
(Jcm −3 ) 1/2 <strong>and</strong> 16.1 (Jcm −3 ) 1/2 , respectively. Therefore, IA <strong>and</strong> LDPE<br />
form a heterogeneous system in the melt. On the other h<strong>and</strong>, it is expected<br />
that some of the peroxides listed in Table 18.5 would dissolve in LDPE.<br />
It is assumed that radicals formed during peroxide decomposition interact<br />
first with LDPE macromolecules, then the formed macroradicals initiate<br />
the grafting reactions with IA. Peroxides, which are easily dissolved<br />
in LDPE, are most efficient in initiating the grafting reactions. 30<br />
It was found that neutralizing agents introduced into the initial reaction<br />
mixture increase the yield of LDPE-g-IA, when the carboxyl groups
622 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
were neutralized partially or totally. As neutralizing agents, zinc oxides<br />
<strong>and</strong> hydroxides as well as magnesium oxides <strong>and</strong> hydroxides can be used. 32<br />
18.2.7 Distribution of the Grafted Groups<br />
There is a lot of research presented in the literature, <strong>and</strong> there is still a<br />
controversy concerning the mechanism <strong>and</strong> the distribution <strong>and</strong> the structure<br />
of the grafted portions on the backbone. This is reviewed in detail by<br />
Moad. 1<br />
18.2.8 Effect of Stabilizers on Grafting<br />
The grafting of maleic anhydride onto poly(ethylene) is fully inhibited by<br />
adding a phenolic stabilizer to the reactive blend. 33<br />
In a system consisting of itaconic acid, linear low density poly(ethylene)<br />
<strong>and</strong> 2,5-dimethyl-2,5-di(tert-butylperoxy)hexane with Irganox<br />
1010 (Ciba Geigy, Switzerl<strong>and</strong>), i.e. the ester of 3,5-di-tert-butyl-4-hydroxyphenyl-propanoic<br />
acid <strong>and</strong> pentaerythritol, the grafting efficiency decreases<br />
slightly.<br />
However, at concentrations of the stabilizer greater than 0.3% some<br />
improvement in the grafting efficiency occurs <strong>and</strong> the melt viscosity is<br />
much lower. 30 The efficiency of stabilizers on the grafting <strong>and</strong> on the<br />
crosslinking also depends on their solubility in the polymer <strong>and</strong> the monomer.<br />
For example, 1,4-dihydroxybenzene has an increased affinity toward<br />
the monomer <strong>and</strong> both reduces the yield of grafting <strong>and</strong> inhibits crosslinking.<br />
34<br />
18.2.9 Radical Grafting of Polyolefins with Diethyl Maleate<br />
The use of maleate esters such as diethyl maleate or dibutyl maleate has<br />
been suggested because of their lower volatility <strong>and</strong> lower toxicity in comparison<br />
to maleic anhydride. However, maleate esters are less reactive towards<br />
free radical addition than maleic anhydride.<br />
Grafting polyolefins with diethyl maleate can be carried out in solution.<br />
However, the use of extruders as reactors has several economic advantages.<br />
The extruder screw is advantageously configured with different<br />
mixing elements after an additional feed zone downstream from the initial<br />
feed port for peroxide <strong>and</strong> diethyl maleate. Further there are no mixing<br />
elements beyond the vent port. Turbine mixing elements are used for the
Grafting 623<br />
improved blending of the low-viscosity initiator <strong>and</strong> the diethyl maleate<br />
into the high-viscosity poly(ethylene). A vacuum vent port is used to eliminate<br />
the unreacted monomer. In the extruder, dicumyl peroxide (DCP), is<br />
used as initiator. 35<br />
The kinetics of the free radical grafting of diethyl maleate (DEM)<br />
onto linear poly(ethylene) initiated by dicumyl peroxide has been studied<br />
by differential scanning calorimetry (DSC). The activation energy E a <strong>and</strong><br />
the order of the reaction n depend on the conditions <strong>and</strong> vary with the feed<br />
composition. The values of E a <strong>and</strong> n increase with increasing DCP/DEM<br />
ratio because of secondary reactions, such as chain extension <strong>and</strong> degradation.<br />
The data can be described by a mathematical model which can<br />
be used to select feed composition <strong>and</strong> process parameters to obtain the<br />
desired products. 36<br />
18.2.10 Inhibitors for the Homopolymerization of Maleic anhydride<br />
In a series of papers, Gaylord showed that various additives are effective<br />
in reducing both the amount of crosslinking <strong>and</strong> chain scission. 37, 38 These<br />
additives include amides, such as N,N-dimethylacetamide, N,N-dimethylformamide,<br />
caprolactam, stearamide, sulfoxides such as dimethyl sulfoxide,<br />
<strong>and</strong> phosphites, such as hexamethylphosphoramide, triethyl phosphite.<br />
The action has been attributed to the electron donating properties of these<br />
compounds. It was shown that these compounds also act as inhibitors of<br />
the homopolymerization of maleic anhydride, thus reducing its grafting<br />
efficiency. However, it seems that these compounds are not effective in<br />
general at least, there was some controversy. 1<br />
18.2.11 Inhibitors for Crosslinking<br />
p-Benzoquinone, triphenyl phosphite <strong>and</strong> tetrachloromethane were found<br />
to be good inhibitors for the crosslinking reaction of LDPE. 39<br />
In the melt grafting of maleic anhydride onto an elastomeric ethylene-octene<br />
copolymer, N,N-dimethylformamide was used as an inhibitor<br />
to reduce the crosslinking reaction. Further N,N-dimethylformamide is a<br />
solvent for peroxide initiator. The melt grafting was carried out in a twinscrew<br />
extruder, in the presence of dicumyl peroxide as an initiator. However,<br />
increasing the initiator concentration increased the degree of grafting,<br />
<strong>and</strong> at the same time, increased the extent of crosslinking. 40
624 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Compound<br />
Table 18.6: Functionalized Peroxides 41<br />
1,1-Dimethyl-3-hydroxybutyl-6-(hydroxy)peroxyhexanoate<br />
1,1-Dimethyl-3-hydroxybutyl-2-(carboxy)perbenzoate<br />
1,1-Dimethyl-3-hydroxybutyl-2-(carboxy)peroxycyclohexanecarboxylate<br />
1,1-Dimethyl-3-hydroxypropyl-3-(carboxy)peroxypropanoate<br />
1,1-Dimethyl-3-hydroxybutyl-3-(carboxy)-5-norbornene-2-ylperoxycarboxylate<br />
18.2.12 Special Initiators<br />
18.2.12.1 Bisperoxy Compounds<br />
The decomposition of the two peroxy groups in bisperoxy compounds is<br />
not concerted. The two peroxy groups decompose independently to yield<br />
a variety of alkoxy <strong>and</strong> alkyl radicals.<br />
18.2.12.2 Functionalized Peroxides<br />
To optimize the chemical compatibility or solubility of the peroxides in a<br />
wide variety of polymeric systems, the organic character of these peroxides<br />
may be tailored by introducing suitable groups.<br />
Functionalized peroxides may be used as crosslinking, grafting <strong>and</strong><br />
curing agents, initiators for polymerization reactions <strong>and</strong> as monomers for<br />
condensation polymerizations to form peroxy-containing polymers, which<br />
in turn can be used to prepare block <strong>and</strong> graft copolymers. Some functionalized<br />
peroxides are shown in Figure 18.3 <strong>and</strong> collected in Table 18.6.<br />
The half-life times of the peroxides at 180°C are ca. 0.27 min for<br />
LUPEROX PMA <strong>and</strong> LUPEROX TA-PMA <strong>and</strong> 0.31 min for Luperco<br />
212-P75 <strong>and</strong> Lupersol 512. The peroxides are assumed to result<br />
in acrylic carboxyl groups <strong>and</strong> propionic carboxyl groups on the tertiary<br />
carbon atoms of poly(propylene) on recombination with the tertiary radicals<br />
formed previously. The highest acidity on the polymer backbone is<br />
obtained with LUPEROX PMA. With respect to the functional radicals,<br />
the peroxides which yield radicals that bear double bonds have a higher<br />
grafting efficiency. It is assumed that the alkenyl radicals have a higher<br />
reactivity with respect to alkyl radicals. Further, the increased grafting efficiency<br />
may arise since macroradicals can add across the double bond of<br />
the alkenyl groups. 42
Grafting 625<br />
CH 3<br />
O<br />
H 3 C C O O C<br />
CH 3<br />
O<br />
CH CH C<br />
OH<br />
Luperox TM PMA<br />
CH 3<br />
O<br />
H 3 C C O O C<br />
CH 3<br />
O<br />
CH 2 CH 2 C<br />
OH<br />
Luperco TM 212-P75<br />
CH 3<br />
CH 2<br />
CH 3<br />
O<br />
C O O C<br />
CH 3<br />
O<br />
CH CH C<br />
OH<br />
Luperox TM TA-PMA<br />
CH 2<br />
CH 3<br />
O<br />
C O O C<br />
CH 3<br />
O<br />
CH 2 CH 2 C<br />
OH<br />
CH 3<br />
Lupersol TM 512<br />
Figure 18.3: Functionalized Peroxides, manufactured by Elf Atochem North<br />
America
626 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
CH 3<br />
O<br />
+<br />
OH<br />
CH<br />
O<br />
CH 2<br />
CH 3<br />
C O O H<br />
+<br />
O<br />
O<br />
CH 3<br />
O<br />
O<br />
HO<br />
O<br />
O<br />
CH 3<br />
O C<br />
CH 3 CH CH 2<br />
CH 3<br />
HO<br />
O<br />
O<br />
Figure 18.4: Reaction of 1,1-Dimethyl-3-hydroxybutyl hydroperoxide with<br />
Maleic anhydride<br />
O<br />
Preparation of Functionalized Peroxides. There are several routes to<br />
preparing functionalized peroxides. 1,1-Dimethyl-3-hydroxybutyl hydroperoxide<br />
reacts with two units of glutaric anhydride or maleic anhydride<br />
in ring opening of the anhydride 43 as shown in Figure 18.4. Similarly,<br />
1,1-dimethyl-3-hydroxybutyl-2-(carboxy)perbenzoate can be prepared<br />
from phthalic anhydride by adding 1,1-dimethyl-3-hydroxybutyl hydroperoxide<br />
in equimolar quantities.<br />
Peroxyketals. The chemical modification of molten poly(ethylene) by<br />
thermolysis of peroxyketals involves the decomposition of three cyclic or<br />
acyclic peroxyketals. An ester function by coupling of an alkyl radical<br />
bearing such a function, arising from the peroxyketals, a polymer radical,<br />
generated from the poly(ethylene), were identified as grafting products. 44<br />
18.2.12.3 Induced Decomposition of Peroxides<br />
Peroxides show an induced decomposition with amino-functional monomers<br />
such as diethylaminoethyl acrylate (DEAEMA) <strong>and</strong> diethylamino-
Grafting 627<br />
Br<br />
Br<br />
Br<br />
Br<br />
H 3 C<br />
H C<br />
C H<br />
CH 3<br />
Br<br />
Br<br />
Br<br />
Br<br />
2,3-Dimethyl-2,3-diphenylbutane<br />
Hexabromocyclododecane<br />
Figure 18.5: Dicumyl <strong>and</strong> Hexabromocyclododecane<br />
ethyl acrylate (TBAEMA). Instead of a peroxide an azo compound can be<br />
used as an radical initiator.<br />
18.2.12.4 Grafting to Poly(ethylene) with Bicumene<br />
Bicumene, i.e., dicumyl or 2,3-dimethyl-2,3-diphenylbutane, can serve as<br />
a radical initiator as an alternative to a peroxide. Compounds of the bicumene-type<br />
also serve as synergists for flame retardants polyolefin by using<br />
them in combination with a known flame-retardant for polyolefin such as<br />
hexabromocyclododecane (c.f. Figure 18.5) <strong>and</strong> 2,3-tris(dibromopropylene)phosphate.<br />
When a peroxide is employed as the reaction initiator, the peroxide<br />
serves as a graft polymerization initiator, but at the same time a portion of<br />
the peroxide induces a crosslinking reaction <strong>and</strong> a decomposition reaction<br />
of the polyolefin. Because of the crosslinking reaction or the decomposition<br />
reaction, the inherent physical properties of polyolefin deteriorate <strong>and</strong><br />
the resulting modified product is unable to maintain the properties of the<br />
polyolefin.<br />
In addition, when the peroxide decomposes as the reaction proceeds,<br />
the decomposition products (e.g., butanol or other decomposition products)<br />
stain the modified product. For example, the modified product yields odor<br />
originating from the decomposition product, or turns to yellow because of<br />
the action of the decomposition product.<br />
The graft polymerization reaction starts more moderately <strong>and</strong> proceeds<br />
more selectively, in comparison to a conventional reaction using peroxide.<br />
Also, the crosslinking reaction or decomposition reaction of poly-
628 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
olefin is less, <strong>and</strong> the resulting modified polyolefin has the excellent physical<br />
properties of the unmodified polyolefin. For instance, when a linear<br />
low density poly(ethylene) is employed, the modified product thereof has<br />
a high mechanical strength at low temperatures. 45<br />
The bicumene-initiated modification of high density poly(ethylene)<br />
at 290°C provides no benefits in terms of selectivity when compared to<br />
a st<strong>and</strong>ard peroxide-based process operating at 180°C. However, the selectivity<br />
of linear low density poly(ethylene) modification is influenced by<br />
chain scission, which counteracted the molecular weight effects of macroradical<br />
combination. 46<br />
As compared with the case of using peroxide, the variation of melt<br />
index caused by the modification is smaller, <strong>and</strong> the modified product obtained<br />
shows a melt index only slightly different from that of the polyolefin<br />
employed as a starting material.<br />
Maleic anhydride is generally employed in the amount of 10 −3 to<br />
10 −5 mol/g of polyolefin. When the amount of maleic anhydride exceeds<br />
10 −3 mol/g, the graft efficiency of maleic acid sometimes decreases, <strong>and</strong><br />
unreacted maleic anhydride remains in a large amount. This results in<br />
an unfavorable effect on the physical properties of the resulting modified<br />
product. When the amount of maleic anhydride is less than 10 −6 mol/g,<br />
the modification with the maleic anhydride is unsatisfactory, <strong>and</strong> accordingly<br />
the resulting modified product does not have sufficiently improved<br />
adhesive properties. 45<br />
The graft polymerization reaction is performed by heating a mixture<br />
of the polyolefin, maleic anhydride <strong>and</strong> the initiator under kneading.<br />
18.2.12.5 Ultrasonic Initiation<br />
The grafting of maleic anhydride onto high density poly(ethylene) also can<br />
be performed through ultrasonic initiation. Obviously, the ultrasonic waves<br />
can decrease the molecular weight of the grafted product <strong>and</strong> increase the<br />
amount of grafted maleic anhydride.<br />
In comparison to the initiation with peroxide, ultrasonic initiation<br />
can prevent the crosslinking reaction by adjusting the ultrasonic intensity.<br />
The mechanical properties of the improved HDPE glass fiber composite<br />
produced by ultrasonic initiatives are higher than in those produced by<br />
peroxide initiatives. 47
Grafting 629<br />
Table 18.7: Use of Maleic anhydride-grafted Linear low density poly(ethylene)<br />
as Compatibilizer<br />
System<br />
Reference<br />
Poly(propylene)/organoclay nanocomposites<br />
48<br />
Low density poly(ethylene)/ethylenevinyl alcohol<br />
49<br />
Poly(propylene)/Poly(styrene)<br />
50<br />
Low density poly(ethylene)/rice starch<br />
51<br />
18.2.13 Maleic anhydride<br />
Maleic anhydride is most frequently used for grafting <strong>and</strong> functionalization<br />
of polyolefins. Many of the features are described in the general sections,<br />
e.g., Section 18.2.2.<br />
Systematic <strong>and</strong> quantitative studies of the graft copolymerization<br />
in batch <strong>and</strong> continuous mixers <strong>and</strong> kinetic data for poly(propylene) <strong>and</strong><br />
maleic anhydride are available. 52 In the melt grafting of maleic anhydride<br />
onto low density poly(ethylene)/poly(propylene) blends, in the presence of<br />
dicumyl peroxide (DCP), the blend had lower viscosity in comparison to<br />
exclusively pure poly(ethylene) under comparable conditions. However,<br />
the grafting degree of the MA grafted LDPE/PP (90/10) blend was almost<br />
the same as or a little higher than that of the MA grafted LDPE. 53<br />
Maleic anhydride can be grafted onto poly(propylene) using benzophenone<br />
(BP) as the photoinitiator. 54 In comparison to thermally initiated<br />
grafting with peroxide initiators, photoinitiated grafting has a higher grafting<br />
efficiency. Maleic anhydride-grafted linear low density poly(ethylene)<br />
(LDPE-g-MA) is widely used as compatibilizer for various applications,<br />
as shown in Table 18.7.<br />
18.2.14 Polyolefins Grafted with Itaconic Acid Derivatives<br />
18.2.14.1 Poly(ethylene) Polyamide 6 Blends<br />
Two-phase blends of polyamide 6 (PA6) <strong>and</strong> low density poly(ethylene)<br />
(LDPE) have been prepared. Here in the course of reactive extrusion, an<br />
in-situ grafting of itaconic acid (IA) on the LDPE takes place. The performance<br />
of blending was tested with neutralization <strong>and</strong> without neutralization<br />
of the acid groups of itaconic acid. 55 The maximum increase with<br />
regard to the mechanical properties was achieved when magnesium hydroxide<br />
was used as a neutralizing agent.
630 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
18.2.14.2 Poly(propylene)<br />
Functionalized poly(propylene) (PP) by radical melt grafting with monomethyl<br />
itaconate or dimethyl itaconate is a compatibilizer in PP/poly(ethylene<br />
terephthalate) (PET) blends. Blends with compositions 15/85 <strong>and</strong><br />
30/70 by weight of PP <strong>and</strong> PET, prepared in a single-screw extruder, revealed<br />
a very fine <strong>and</strong> uniform dispersion of the PP phase compared to the<br />
respective non-compatibilized blends.<br />
An improved adhesion between the two phases is shown. Dimethyl<br />
itaconate as compatibilizer derived agent exhibits only a small activity to<br />
increase the impact resistance of PET in PP/PET blend. However, monomethyl<br />
itaconate is active in this respect. This finding is attributed to the<br />
hydrophilic nature of monomethyl itaconate. The tensile strength of PET<br />
in non-compatibilized blends gradually decreases with increasing content<br />
of PP. Blends containing functionalized PP exhibit, in general, higher values.<br />
56<br />
18.2.15 Imidized Maleic Groups<br />
The chemical modification of swollen HDPE particles in near critical propane<br />
seems to be much more effective in avoiding crosslinking than the conventional<br />
modification in the melt phase.<br />
High density poly(ethylene) grafted with 0.17% maleic anhydride<br />
(PE-g-MA) can be additionally modified with 1,4-diaminobutane (DAB).<br />
After formation of amic acid groups, the excess of diaminobutane is extracted<br />
with a near critical propane-ethanol mixture.<br />
Finally, the obtained PE-g-MA-DAB is imidized to the corresponding<br />
imide (PE-g-MI) in the melt. The obtained PE-g-MI shows no increased<br />
gel content with respect to the initial PE-g-MA. It appears that<br />
PE-g-MI samples react with the anhydride groups of a styrene/maleic anhydride<br />
copolymer (SMA) during melt blending of SMA with PE-g-MI,<br />
while the PE-g-MA do not react. 57<br />
18.2.16 Oxazoline-modified Polyolefins<br />
The free radical induced grafting of 2-isopropenyl-2-oxazoline (IPO) onto<br />
PP has been reported. 58
18.2.17 Modification of Polyolefins with Vinylsilanes<br />
Grafting 631<br />
Vinylsilanes, e.g., vinyltrimethoxysilane (VTMS) do not readily homopolymerize.<br />
The modification of polyolefins with vinylsilanes, such as vinyltrimethylsilane,<br />
vinyltriethylsilane, or 3-(trimethoxysilyl)propyl methacrylate<br />
aims to the preparation of a moisture curable crosslinked polyolefins.<br />
For example, the silane grafting of a metallocene ethylene-octene<br />
copolymer is carried out in a twin-screw extruder, in the presence of vinyltrimethoxysilane<br />
<strong>and</strong> dicumyl peroxide. 17 These materials are used in the<br />
manufacture of electrical cables.<br />
18.2.17.1 Vinyltriethoxysilane<br />
Bicumene initiates the grafting of vinyltriethoxysilane (VTEOS) to poly-<br />
(ethylene) efficiently over an uncommonly large range of operating temperatures.<br />
The analysis of kinetics of bicumene decomposition suggests<br />
that the initiation occurs via an autoxidation mechanism that is facilitated<br />
by the interaction of cumyl radicals with oxygen. 46<br />
The analysis of poly(ethylene-g-vinyltrimethoxysilane) by differential<br />
scanning calorimetry-successive self-nucleation <strong>and</strong> annealing<br />
(DSC-SSA) indicated that the distribution of pendant alkoxysilane grafts<br />
amongst polymer chains is not uniform. Fractionation <strong>and</strong> characterization<br />
of a graft-modified model compound, tetradecane-g-VTMS, showed that<br />
the composition distributions were influenced strongly by intramolecular<br />
hydrogen atom abstraction. It yields multiple grafts per chain as single<br />
pendant units <strong>and</strong> oligomeric grafts. The chain transfer to the methoxy<br />
substituent of VTMS grafts contributes significantly to the product distribution.<br />
59<br />
The selectivity for the ratio of grafting to crosslinking shows a considerable<br />
scope for optimization through variation of monomer <strong>and</strong> peroxide<br />
loadings in the case of VTEOS as modifier, in contrast to maleic<br />
anhydride. 60<br />
18.2.18 Ethyl Diazoacetate-modified Polyolefins<br />
Ethyl diazoacetate <strong>and</strong> chloroethyl diazoacetate is inserted by a carbene<br />
insertion mechanism at 210°C. No radical initiator is needed, however the<br />
grafting efficiency is small.<br />
61, 62
632 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
H 3 C<br />
C<br />
H 3 C<br />
CH 3<br />
HO<br />
H 3 C<br />
C<br />
H 3 C CH 3<br />
CH 2 O CH CH 2<br />
DBBA<br />
O<br />
CH 2<br />
CH C<br />
O<br />
O<br />
CH 2<br />
CH 2<br />
CH C O CH 2<br />
C CH 2 CH 3<br />
CH 2<br />
CH C O CH 2<br />
O<br />
TRIS<br />
Figure 18.6: 3,5-Di-tert-butyl-4-hydroxybenzyl acrylate (DBBA) <strong>and</strong> 1,1,1-Trimethylolpropane<br />
triacrylate (TRIS)<br />
18.2.19 Grafting Antioxidants<br />
Routes for grafting antioxidants onto polyolefins with high grafting yields<br />
have been reported. The antioxidant 3,5-di-tert-butyl-4-hydroxybenzyl<br />
acrylate (DBBA) reacts with the trifunctional coagent 1,1,1-trimethylolpropane<br />
triacrylate (TRIS), c.f. Figure 18.6, in the presence of a small<br />
concentration of a free-radical initiator in a poly(propylene) melt during<br />
processing.<br />
The major reaction is a homopolymerization of the antioxidant in<br />
the absence of TRIS. This results in low grafting levels. However, in the<br />
presence of TRIS, more than 90% grafting efficiency of DBBA on the polymer<br />
is monitored, 6% of DBBA is used. The mechanism of the grafting<br />
reaction could be established with decalin, used as a hydrocarbon model<br />
compound. 15 The decalin adds with the hydrogen atom on the bridge to<br />
the double bond of DBBA.<br />
Quinoneimines containing an N-p-hydroxyphenyl <strong>and</strong> an N-p-aminophenyl<br />
substituent have a high antioxidant efficiency when added to<br />
isoprene rubber (IR), styrene butadiene rubber (SBR), ethylene/propylene<br />
rubber (EPR), <strong>and</strong> ethylene propylene diene monomer (EPDM) rubbers,
Grafting 633<br />
H 3 C<br />
C<br />
H 3 C<br />
CH 3<br />
R<br />
O<br />
O<br />
+<br />
H 2 N<br />
R’<br />
H 3 C<br />
C<br />
H 3 C<br />
CH 3<br />
H 3 C<br />
C<br />
H 3 C<br />
CH 3<br />
R<br />
O<br />
N<br />
R’<br />
H 3 C<br />
C<br />
H 3 C<br />
CH 3<br />
Figure 18.7: Synthesis of Quinoneimines<br />
because they add to the allylic −CH of the polymer giving active adducts.<br />
The synthesis of the quinoneimines is shown in Figure 18.7. The retention<br />
of the protective activity after extraction of the material indicates the<br />
grafting of these compounds during the thermal or mechanical processing<br />
of the rubbers. 63<br />
18.2.20 Comonomer Assisted Free Radical Grafting<br />
The idea of using styrene as a comonomer originated from a detailed analysis<br />
of the mechanism of free radical grafting. To obtain high graft efficiency,<br />
together with a reduced degradation of polymer, it is essential that<br />
the macroradicals in the backbone react with the grafting monomers before<br />
they undergo chain scission of the backbone. If the primary monomer<br />
is not sufficiently reactive towards the macroradicals, it is helpful to add<br />
another monomer that reacts with the macroradicals faster than primary<br />
monomer. A further requirement is that the resulting pendent free radicals<br />
of the secondary monomer copolymerize readily with the primary monomer.<br />
It was shown that the addition of styrene can improve the graft efficiency<br />
of monomers such as hydroxyethyl methacrylate (HEMA) <strong>and</strong>
634 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
N<br />
C<br />
O<br />
CH 2<br />
CH 2<br />
+<br />
HO<br />
O<br />
C<br />
O<br />
C<br />
N<br />
H<br />
O<br />
CH 2 CH 2 O C<br />
Figure 18.8: Ring Opening of a Pendant Oxazoline Group<br />
methyl methacrylate (MMA), glycidyl methacrylate (GMA), but not vinyl<br />
acetate (VAc) <strong>and</strong> ricinoloxazoline maleate (OXA). This is due to the fact<br />
that styrene copolymerizes readily with HEMA, MMA, <strong>and</strong> GMA, but not<br />
with VAc <strong>and</strong> OXA. The ring opening of a pendant oxazoline group is<br />
shown in Figure 18.8.<br />
Ricinoloxazoline maleate is a bifunctional compatibilizer agent. It<br />
can be grafted with the vinyl function of the maleate unit onto a poly-<br />
(propylene) site by usual radical grafting, thus becoming oxazoline groups<br />
attached to the poly(propylene) chain. The oxazoline group can be reacted<br />
with the carboxyl groups of poly(butylene terephthalate). 16<br />
18.2.20.1 Styrene-assisted Grafting<br />
Maleic anhydride. The low reactivity of MA with respect to free-radical<br />
polymerization is inherently due to its structural symmetry <strong>and</strong> the deficiency<br />
of the electron density around the double bond.<br />
It is clear that the addition of a monomer capable of donating electrons,<br />
i.e., an electron-rich comonomer, would activate an electron deficient<br />
monomer like MA by changing the electron density of the π-bond.<br />
The addition of styrene to a melt grafting system as a comonomer<br />
of maleic anhydride can significantly enhance the graft degree onto poly-<br />
(propylene). The maximum graft degree is obtained when the molar ratio<br />
of maleic anhydride to styrene is approximately 1:1.<br />
Styrene improves the grafting reactivity of maleic anhydride <strong>and</strong><br />
also reacts with maleic anhydride to form a styrene/maleic anhydride co-
Grafting 635<br />
polymer (SMA) before grafting onto the poly(propylene) backbone.<br />
When the concentration of maleic anhydride is higher than that of<br />
styrene, some maleic anhydride monomer reacts with styrene to form<br />
SMA, but others can directly graft onto macroradicals on the poly(propylene)<br />
chain. When the amount of styrene added is higher than that of<br />
maleic anhydride, a part of the styrene monomer may preferentially react<br />
with the macroradicals to form macroradicals with styryl ends, while<br />
others copolymerize with maleic anhydride to yield SMA. 10<br />
On the other h<strong>and</strong>, styrene is ineffective as comonomer for maleate<br />
esters grafting onto PP. 64 This arises from the low affinity of the styryl<br />
radical towards the maleate ester species. This could be predicted from the<br />
critical inspection of the monomer reactivity ratios of styrene <strong>and</strong> maleic<br />
esters.<br />
Glycidyl Methacrylate. The reactivity of glycidyl methacrylate (GMA)<br />
in free radical grafting onto poly(propylene) (PP) is low. However, adding<br />
styrene as a comonomer for glycidyl methacrylate increases both the rate<br />
<strong>and</strong> grafting efficiency. Further the degradation of PP is reduced. It is believed<br />
that when styrene is added to such a grafting system, styrene reacts<br />
first with PP macroradicals to form pendent styryl radicals. These styryl<br />
radicals are the starting point for a copolymerization with GMA to form a<br />
grafted PP. 13<br />
Poly(propylene) functionalized with glycidyl methacrylate has been<br />
used for the compatibilization of poly(propylene) <strong>and</strong> poly(butylene terephthalate)<br />
blends. 65 Similar studies have been done for the grafting of<br />
glycidyl methacrylate onto linear low density poly(ethylene) (LLDPE). 14<br />
18.2.20.2 Increasing the Grafting Efficiency with Comonomers<br />
The mechanisms that result in higher grafting yields by the addition of<br />
comonomers can be attributed to 1<br />
• Longer chain grafts,<br />
• More grafting sites,<br />
• Use of polyvinyl monomers.<br />
Longer chain grafts appear to be the favored alternating copolymerization<br />
of electron donor-electron acceptor forming monomer pairs. Examples are<br />
styrene, <strong>and</strong> maleic anhydride. More grafting sites emerge by a more efficient<br />
addition of the macroradicals on the backbone by the addition of
636 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 18.8: Experimental Techniques for the Characterization of Modified<br />
Polyolefins<br />
Method<br />
Remarks<br />
Titration<br />
Maleic anhydride, glycidyl units<br />
FTIR spectroscopy Most widely used method<br />
NMR spectroscopy Chemical shifts are very sensitive to the<br />
chemical environment<br />
13 C NMR spectroscopy Poor sensitivity<br />
a comonomer. Polyfunctional monomers effect presumptive branching or<br />
crosslinking sites when once grafted onto the backbone. In this way a star<br />
shaped or comb shaped grafting center may emerge. An example for this<br />
concept is the use of a triacrylate monomer as comonomer. 66<br />
18.2.21 Radiation Induced Grafting in Solution<br />
A suitable solvent for the radiation induced graft copolymerization of styrene<br />
<strong>and</strong> maleic anhydride (Sty/MA) binary monomers onto high density<br />
poly(ethylene) (HDPE) is acetone. Untreated <strong>and</strong> treated grafted HDPE<br />
membranes have potential applications in dialysis. 67<br />
The hydrophilicity of the membrane, the degree of grafting <strong>and</strong> the<br />
molecular weight <strong>and</strong> chemical structure of the metabolites, such as urea,<br />
creatinine, uric acid, glucose, <strong>and</strong> phosphate salts, have a great influence<br />
on the transport properties of the membrane. The permeability increases<br />
with the degree of grafting. Basic metabolites show higher permeation<br />
rates through the modified membrane as acidic metabolites, in particular<br />
phosphate salts. The permeabilities of high molecular weight compounds<br />
are low.<br />
18.2.22 Characterization of Polyolefin Graft Copolymers<br />
The characterization of the grafted functionality in modified polyolefins is<br />
difficult because the small number of modified units are overwhelmed by<br />
the normal polyolefin repeat units.<br />
The content of modified units is typically only about one to five<br />
modified units per molecule in a polymer of typical molecular weight of 20<br />
to 40 kDalton. 1, 2 Some experimental techniques to characterize modified<br />
polyolefins are summarized in Table 18.8.
Table 18.9: <strong>Polymers</strong> Used for Grafting<br />
Grafting 637<br />
Polymer Grafting Agent Reference<br />
Poly(styrene) Maleic anhydride<br />
68<br />
Poly(vinyl chloride) n-Butyl methacrylate<br />
69<br />
Poly(alkylene terephthalate) Nadic anhydride<br />
70<br />
Starch Vinyl acetate<br />
71<br />
Starch Methyl acrylate<br />
72<br />
18.2.23 PVC/LDPE Melt Blends<br />
In blends of a low density poly(ethylene) (LDPE) with polyvinyl chloride<br />
(PVC) during melt blending, chemical reactions take place. 73 This is indicated<br />
by changes in the molecular weight, M n <strong>and</strong> M w number-average<br />
molecular weight, the polyene <strong>and</strong> the carbonyl indices, color changes,<br />
<strong>and</strong> the changes of the glass transition <strong>and</strong> decomposition temperatures.<br />
By mixing of LDPE to PVC <strong>and</strong> melt blending, short-chain LDPE grafted<br />
PVC (s-LDPE-g-PVC) copolymers are formed. On the other h<strong>and</strong>, the<br />
dehydrochlorination reaction of PVC was suppressed.<br />
18.3 OTHER POLYMERS<br />
Table 18.9 summarizes polymer types other than polyolefins that have been<br />
used for grafting other units.<br />
18.3.1 Poly(styrene) Functionalized with Maleic anhydride<br />
Maleic anhydride (MA) can be grafted to poly(styrene) (PS) by reactive<br />
extrusion in the presence of a free-radical initiator, namely 1,3-Bis(tertbutylperoxyisopropyl)benzene.<br />
Its half-life is about 2.5 min at 180°C. The<br />
introduction of the maleic anhydride units in PS proved to be very effective<br />
for controlling the morphology of blends of PA6 with modified PS. The<br />
rheological properties of the blends indicate the formation of long branching<br />
between the amine end groups of PA6 <strong>and</strong> the maleic anhydride unit of<br />
maleic anhydride grafted poly(styrene) (MPS) during melt mixing. 68<br />
18.3.2 Multifunctional Monomers for PP/PS Blends<br />
Polyolefins, do not have reactive functionalities. There are two commonly<br />
used approaches for compatibilization in reactive extrusion. 74
638 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
1. In the two-step process, polymers are functionalized selectively<br />
in the first step, <strong>and</strong> then blended in an extruder in the second<br />
step. The grafting reaction should occur between the functionalized<br />
groups during blending, <strong>and</strong> graft co-polymers are formed<br />
in-situ.<br />
2. In the one-step process, low molecular weight compounds are<br />
added into the melted blends to initiate grafting <strong>and</strong> coupling reactions<br />
at the phase interface to form graft or block copolymers<br />
during the extrusion process.<br />
Peroxides cause serious chain scission of the PP backbone, which<br />
affects the properties of the alloys. Multifunctional monomers, such as glycol<br />
trilinoleate (GTL), trimethylolpropane triacrylate (TMPTA), diethylene<br />
glycol diacrylate (DEGDA) or tripropylene glycol diacrylate (TPGDA) in<br />
combination with dicumyl peroxide (DCP) can suppress the PP degradation<br />
efficiently, <strong>and</strong> promote the grafting reaction to some extent at the<br />
same time. GTL is prepared by the esterification of glycerol with linoleic<br />
acid. 74<br />
18.3.3 Poly(ethylene-co-methyl acrylate)<br />
Maleic anhydride can be melt-grafted onto poly(ethylene-co-methyl acrylate).<br />
The grafting is enhanced with a comonomer, i.e., divinylbenzene or<br />
vinyl-4-tert-butylbenzoate. A suitable radical initiator is 1,1-di(tert-butylperoxy)-3,3,5-trimethylcyclohexane<br />
(LUPERSOL 231). The processing<br />
temperature of the internal batch mixer is at 140°C. It was observed<br />
that styrene <strong>and</strong> vinyl-4-tert-butylbenzoate can significantly increase the<br />
amount of anhydride grafted. The styrene comonomer system is most efficient.<br />
75 The use of 1-dodecene in this system showed primarily a plasticizer<br />
effect.<br />
18.3.4 n-Butyl methacrylate Grafted onto Poly(vinyl chloride)<br />
Melt grafting of n-butyl methacrylate onto poly(vinyl chloride) was<br />
achieved by a melt mixing process with a free-radical initiator. 69 A maximum<br />
of 14% graft was obtained. The graft copolymer showed significant<br />
improvement in processability <strong>and</strong> both thermal <strong>and</strong> mechanical properties.
Grafting 639<br />
18.3.5 Starch Esterification<br />
Starch esters with low degrees of substitution are prepared in aqueous media<br />
by batch methods. 76 Extrusion is not used widely for modification of<br />
starch, however, it has great potential. Extruders have been used to manufacture<br />
carboxymethylated <strong>and</strong> cationic potato starch, starch phosphates,<br />
anionic starch, <strong>and</strong> oxidized starches. 77–80<br />
Starch esters can be synthesized by extruding 70% amylose starch<br />
with fatty anhydrides <strong>and</strong> sodium hydroxide as catalyst in a single-screw<br />
extruder. The sodium hydroxide neutralizes the organic acids formed in the<br />
course of the reaction. Acetic anhydride, propionic anhydride, heptanoic<br />
anhydride, <strong>and</strong> palmitic anhydride have been used. 81 The degrees of substitution<br />
of esterified starch can be determined by hydrolyzing substituted<br />
groups with NaOH <strong>and</strong> then titrating back with acid. The degree of substitution<br />
coincides with the expected value from the monomer feeds. Some<br />
molecular weight reduction of the amylopectin fraction was detected in the<br />
esterified products from cornstarch with a 70% amylose content. Lower<br />
molecular weights <strong>and</strong> higher levels of anhydride resulted in the greatest<br />
reduction in starch molecular weight.<br />
The acid esters decrease the hydrophilic character of the starch. The<br />
introduction of heptanoic anhydride <strong>and</strong> palmitic anhydride result in a<br />
higher water absorption index. This is explained by the disruption of the<br />
crystalline structure of the starch. By disrupting the crystalline structure of<br />
the starch, the opportunity for hydrogen-bonding between starch <strong>and</strong> water<br />
is increased. Clearly, the heptanoic <strong>and</strong> palmitic acid residues provide a<br />
more significant steric hindrance for the formation of starch crystals than<br />
the smaller acetic <strong>and</strong> propionic acid residues.<br />
Another approach for the acetylation of starch is the use of vinyl<br />
acetate <strong>and</strong> sodium hydroxide. 71 The acetylation reaction is accompanied<br />
by the hydrolysis of vinyl acetate <strong>and</strong> a consecutive hydrolysis reaction of<br />
the acetylated starch. The degree of substitution could be varied from 0.05<br />
to 0.2.<br />
18.3.6 Starch Grafted Acrylics<br />
Starch graft poly(methyl acrylate) (S-g-PMA) could be prepared from an<br />
aqueous cornstarch slurry <strong>and</strong> methyl acrylate by the initiation with ceric<br />
ions. At the end of the reaction, an additional small amount of ceric ion solution<br />
was added. After this addition no unreacted methyl acrylate mono-
640 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
mer remained. 72 The grafted starch is intended for the use as loose-fill<br />
foam. This type of loose-fill foam has a better moisture <strong>and</strong> water resistance<br />
than other starch-based materials.<br />
Graft copolymers of starch <strong>and</strong> poly(acrylamide) could be prepared<br />
by reactive extrusion with ammonium persulfate as initiator. 82<br />
18.3.7 Thermoplastic Phenol/Formaldehyde <strong>Polymers</strong><br />
Phenol/formaldehyde resins with high viscosity are needed in reactive extrusion<br />
with poly(propylene) to establish a favorable viscosity ratio. Most<br />
commercially available phenol/formaldehyde resins have a molar mass of<br />
0.5 to 1 kDalton. Only thermoplastic phenol/formaldehyde polymers of<br />
the novolak type meet the requirement of avoiding crosslinking in the extruder.<br />
High molecular weight novolak-type resins can be obtained by adjusting<br />
the ratio of formaldehyde to the phenol near unity. 83<br />
18.3.8 Polyesters <strong>and</strong> Polyurethanes<br />
A number of techniques for polymerizing radical polymerizable monomers<br />
with polyester resins <strong>and</strong> polyurethane resins to obtain graft or block reaction<br />
products have been published. The graft or block reaction products<br />
have been studied to improve, for example, the impact resistance of<br />
molding compounds by using them as a compatibilizer, the adhesiveness<br />
of paints <strong>and</strong> adhesives to substrates, the curing property of the paints <strong>and</strong><br />
adhesives, <strong>and</strong> the dispersibility of pigments. 84<br />
The modification of high molecular weight polyesters introduces<br />
polymerizable unsaturated double bonds into the main chain or into the<br />
molecular terminal groups. The double bonds can be polymerized with<br />
radical polymerizable monomers by graft or block polymerization. Similarly,<br />
graft or block modifications for polyurethane can be achieved.<br />
When a high molecular weight polyester or polyurethane is grafted<br />
for the modification, crosslinking between the polyester molecules or the<br />
polyurethane molecules is more likely.<br />
18.3.8.1 Polyesters<br />
In the case of polyesters, the sum of polymerizable unsaturated double<br />
bonds is desirably up to 20 mol-% of the total acid components <strong>and</strong> diol
Grafting 641<br />
components. When the sum exceeds 20 mol-%, various properties of the<br />
base resin itself are largely reduced.<br />
18.3.8.2 Polyester Polyurethanes<br />
The polyester polyurethanes should contain up to 30 polymerizable unsaturated<br />
double bonds in one molecule.<br />
18.3.8.3 Radical Polymerizable Monomers<br />
Radical polymerizable monomers are a mixture of an electron accepting<br />
monomer <strong>and</strong> an electron donor monomer. This combination allows controlling<br />
the gelation, even if the resin has a very large amount of unsaturated<br />
bonds. Electron donor monomers are styrene, α-methyl styrene, tertbutyl<br />
styrene, <strong>and</strong> N-vinyl pyrrolidone. 85 Electron accepting monomers<br />
are fumaric acid, monoesters, <strong>and</strong> diesters of fumaric acid.<br />
Basically gelation can be avoided by a dilution of the polymeric<br />
vinyl groups by monomeric vinyl groups that are more prone to copolymerize.<br />
18.3.8.4 Grafting Reaction<br />
This technique is a graft polymerization of the polymerizable unsaturated<br />
double bond existing in the base resin, i.e., the main chain with the radical<br />
polymerizable monomers. The graft polymerization reaction is performed<br />
by reacting the base resin, which is dissolved in an organic solvent, with a<br />
mixture of the radical polymerizable monomers <strong>and</strong> a radical initiator.<br />
Suitable radical initiators are organic peroxides <strong>and</strong> organic azo compounds.<br />
The organic peroxides include dibenzoyl peroxide <strong>and</strong> tert-butylperoxypivalate<br />
<strong>and</strong> the organic azo compounds include 2,2 ′ -azobis(isobutyronitrile)<br />
<strong>and</strong> 2,2 ′ -azobis(2,4-dimethylvaleronitrile). A chain transfer<br />
agent such as octyl mercaptane, dodecyl mercaptane, 2-mercaptoethanol,<br />
<strong>and</strong> α-methyl styrene dimer may be used to control the grafted chain<br />
length.<br />
The solvents that can be utilized include methylethylketone, methylisobutylketone,<br />
cyclohexanone, toluene, xylene, ethyl acetate, <strong>and</strong> butyl<br />
acetate. The solvent itself should neither decompose the radical initiator by<br />
induced decomposition nor create a combination with the initiator which
642 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
O<br />
+<br />
O<br />
O<br />
H<br />
O<br />
enophil<br />
H<br />
O<br />
ene<br />
Figure 18.9: Basic Mechanism of the Ene Reaction<br />
causes a danger of explosion that has been reported between specific organic<br />
peroxides <strong>and</strong> specific ketones. Furthermore, it is important that the<br />
solvent has a suitably lower chain transfer constant as a reaction solvent<br />
for the radical polymerization. 84<br />
18.3.9 Polyacrylic Hot-melt Pressure-sensitive Adhesive<br />
A polyacrylic hot-melt pressure-sensitive adhesive is prepared as follows.<br />
A copolymer consisting of acrylic acid, tert-butyl acrylamide, maleic anhydride,<br />
2-ethylhexyl acrylate, n-butyl acrylate is manufactured in acetone/-<br />
isopropanol solution, with 2,2 ′ -azobis(2-ethylpropionitrile) as initiator in a<br />
batch reactor.<br />
This polymer contains anhydride groups that are useful for coupling.<br />
The polymer is then degassed from the solvent in an extruder. In the next<br />
step, the acrylic hot-melt is compounded with 2-hydroxypropyl acrylate.<br />
Pendent acrylate groups are formed in this way. This offers the advantage<br />
of very gentle crosslinking methods, since crosslinking can be carried out<br />
directly by way of the installed acrylate groups. The hot-melt exhibits<br />
viscoelastic behavior at room temperature. 86<br />
18.4 TERMINAL FUNCTIONALIZATION<br />
18.4.1 Ene Reaction with Poly(propylene)<br />
Polyolefins prepared with Ziegler-Natta processes or metallocene catalysts<br />
may carry olefinic end groups. Olefinic end groups are also introduced by<br />
melt degradation.<br />
A poly(propylene) functionalized at the end groups with anhydride<br />
can be obtained via the Alder-ene reaction from a low molecular weight
Grafting 643<br />
amorphous poly(propylene) by reactive extrusion. The Alder-ene reaction<br />
is a pericyclic reaction with a 6-center intermediate. It involves the reaction<br />
of an ene <strong>and</strong> a enophil. The ene moiety in the Alder-ene reaction is a<br />
double bond with an allylic hydrogen. The basic mechanism is shown in<br />
Figure 18.9.<br />
The ene reaction is reversible. 87 However, the reverse reaction seems<br />
to be not a simple retro-ene process. The rate of the Alder-ene reaction depends<br />
on the acidity <strong>and</strong> basicity of ene <strong>and</strong> enophile, respectively. Lewis<br />
acids, like SnCl 4 ,TiCl 4 , <strong>and</strong> AlCl 3 develop fumes of hydrochloric acid during<br />
reaction. However, a less reactive Lewis acid, SnCl 2·2 H 2 O, can also<br />
catalyze the reaction without the drawback of developing HCl.<br />
The reaction is complete at 230°C within 5 min in the presence of<br />
a stable radical, such as 2,2,6,6-tetramethyl-1-piperidinyloxy (TEMPO),<br />
which acts as a free radical scavenger. This prevents the maleic anhydride<br />
from being grafted onto the backbone of the poly(propylene).<br />
4, 88<br />
The maleation of polypropylene by reactive extrusion via the Alderene<br />
reaction produces a terminal functionality of the polymer without significant<br />
chain scission.<br />
18.4.2 Styrene-butadiene Rubber<br />
The end capping of living anions of poly(styrene-butadiene) can be done<br />
with polymeric terminator molecules. A polar functional terminator is<br />
a block copolymer of poly(ethylene glycol) <strong>and</strong> poly(dimethylsiloxane)<br />
(PEG-PDMS) containing a chlorosilyl moiety at one chain end. This polymer<br />
is synthesized by two-step hydrosilylation reaction. 89 The PEG-PDMS<br />
end groups behave as polar functional groups, showing an increase of the<br />
glass transition temperature <strong>and</strong> storage modulus in a composite of endcapped<br />
SBR with silica particles.<br />
18.4.3 Diels-Alder Reaction<br />
A benzocyclobutene (BCB) capped polymer can be used to react in a Diels-Alder<br />
reaction with another polymer bearing a dienophile. 90 4-(3-iodopropyl)benzocyclobutene<br />
was used to terminate an anionic polymerization<br />
of styrene to give a poly(styrene) end-capped with BCB.<br />
A copolymer of 1-hexene <strong>and</strong> 7-methyl-1,6-octadiene was prepared<br />
by Ziegler-Natta polymerization, with the pendant double bonds intended<br />
as the grafting sites. The reaction is illustrated in Figure 18.10.
644 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
CH<br />
CH 2<br />
CH 2<br />
CH 2<br />
CH<br />
+<br />
C<br />
H 3 C CH 3<br />
H<br />
H 3 C<br />
CH<br />
CH 2<br />
CH 2<br />
CH 2<br />
C<br />
C<br />
CH 3<br />
Figure 18.10: Grafting of an Isomerized Benzocyclobutene Unit to a Polyolefin<br />
Dienophile 90<br />
18.5 GRAFTING ONTO SURFACES<br />
18.5.1 Grafting onto Poly(ethylene)<br />
18.5.1.1 Sulfonic Acid Groups<br />
In order to introduce sulfonic acid groups on poly(ethylene), poly(ethylene)<br />
samples are irradiated with UV light in a gas atmosphere containing<br />
SO 2 <strong>and</strong> air to achieve a photosulfonation of the surface. The surface modification<br />
is carried out under atmospheric pressure <strong>and</strong> is considered to be<br />
an inexpensive alternative to plasma modification techniques.<br />
The hydrophilicity of the PE surface increases considerably compared<br />
to unreacted PE. The depth of photomodification reached several µ.<br />
Because of the large depth of modification, the process may also be useful<br />
for the modification of membranes. In combination with projection lithography<br />
the process could be suitable for the manufacture of gratings in<br />
thin polymer films, as required for holographic recordings <strong>and</strong> distributed<br />
feedback lasers. 91<br />
18.5.1.2 Sulfate Groups<br />
Sulfate groups at the surface of poly(ethylene) are introduced by immobilizing<br />
a precoated layer of either sodium 10-undecenyl sulfate (SUS) or<br />
sodium dodecyl sulfate (SDS) on the polymeric surface by means of an<br />
argon plasma treatment. SUS is synthesized by sulfating 10-undecene-<br />
1-ol with the pyridine-SO 3 complex. The presence of sulfate groups at the<br />
polymeric surfaces was confirmed by X-ray photoelectron spectroscopy
Grafting 645<br />
(XPS). The presence of an unsaturated bond in the alkyl chain of the surfactant<br />
improved the efficiency of the immobilization process. About 25%<br />
of the initial amount of sulfate groups in the precoated layer was retained<br />
at the PE surface for SUS, but only 6% for SDS. 92<br />
18.5.1.3 Photochemical Bromination<br />
The gas phase bromination of poly(ethylene), poly(propylene) <strong>and</strong> poly-<br />
(styrene) film surfaces by a free-radical photochemical mechanism occurs<br />
with high regioselectivity. The surface bromination is accompanied by a<br />
simultaneous dehydrobromination. This results in the formation of long<br />
sequences of conjugated double bonds. Thus, the brominated polyolefin<br />
surface contains bromide moieties in different chemical environments. 93<br />
In contrast, the gas phase free radical photochemical chlorination of<br />
polyolefin films proceeds in a rather r<strong>and</strong>om way <strong>and</strong> is also accompanied<br />
by simultaneous dehydrochlorination.<br />
18.5.1.4 Poly(thiophene)<br />
Poly(thiophene) (PT) can be grafted on a PE film using three reaction steps.<br />
1. PE films are brominated in the gas phase, yielding PE-Br.<br />
2. A substitution reaction of PE-Br with 2-thiophene thiolate anion<br />
gives the thiophene-functionalized PE.<br />
3. PT is grafted on the PE surface using chemical oxidative polymerization<br />
to give PE-PT.<br />
The polymerization is performed in a suspension solution of anhydrous<br />
FeCl 3 in CHCl 3 , yielding a reddish PE-PT film after dedoping with<br />
ethanol. Infrared spectroscopy reveals that the PT is grafted on PE in the<br />
2,5-position.<br />
SEM imaging shows isl<strong>and</strong>s of PT on the PE film. The thickness of<br />
the isl<strong>and</strong>s is in the range of 120 to 145 nm. The conductivity of these thin<br />
films is in the range of 10 −6 Scm −1 , which is a significant increase from<br />
the value of 10 −14 Scm −1 measured for an ungrafted PE film. 94<br />
18.5.1.5 Acrylics<br />
Ion beam-modified poly(ethylene) was exposed to the solutions of acrylic<br />
acid, acrylonitrile, <strong>and</strong> bromine. 95 The chemical <strong>and</strong> structural changes
646 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
were examined using spectroscopic techniques, electronparamagnetic resonance,<br />
<strong>and</strong> Rutherford back-scattering techniques.<br />
Acrylic acid, acrylonitrile, <strong>and</strong> bromine react with radicals <strong>and</strong> conjugated<br />
double bonds created by the ion irradiation in the poly(ethylene).<br />
The reactions in the ion beam-modified surface layer may lead to the creation<br />
of a grafted surface layer with a thickness of up to 150 nm.<br />
Surface photo grafting of high density poly(ethylene) (HDPE) powder<br />
can be achieved with a pretreated HDPE surface by benzophenone<br />
(BP). Onto such a surface, acrylic acid can be graft copolymerized by<br />
photo grafting in the vapor phase. 96 The most suitable reaction temperature<br />
is 90°C. The grafting degree can reach a comparable high value of<br />
10%.<br />
18.5.1.6 Siloxane<br />
The dyeing properties on high-strength <strong>and</strong> high modulus poly(ethylene)<br />
fibers are improved by building up a layer of a polysiloxane network. The<br />
grafting of siloxane onto poly(ethylene) proceeds first via a treatment with<br />
peroxide. Hydrogen peroxide in o-xylene emulsion is emulsified by sonication.<br />
The emulsion is effective for introduction of hydroxide groups onto<br />
the poly(ethylene) fiber surface. The treatment does not influence the tensile<br />
strength of the fiber. A polysiloxane network can be built up on the<br />
fiber surface by treating the surface with a (3-aminopropyl)triethoxysilane<br />
(APS) solution. 97 In fact, this method can be used to dye a poly(ethylene)<br />
fiber surface.<br />
18.5.1.7 Silicone<br />
The surface graft copolymerization of hydrogen silicone fluid onto a low<br />
density poly(ethylene) (LDPE) film through corona discharge shows an<br />
improved hydrophobicity of the grafted LDPE films. However, the mechanical<br />
properties decrease slightly. Thus there is evidence that HSF can<br />
be graft copolymerized onto an LDPE film surface through corona discharge.<br />
98<br />
18.5.1.8 Surface Crosslinking<br />
Ultra-high molecular weight poly(ethylene) (UHMWPE) can be crosslinked<br />
at the surface by irradiation with electron beams. 99 Attenuated total
Grafting 647<br />
reflectance Fourier transform infrared spectroscopy (ATR-FTIR) infrared<br />
techniques suggest that the irradiation in air atmosphere introduced hydroperoxide<br />
groups into the polymer without formation of any other oxygencontaining<br />
groups.<br />
The generated hydroperoxides could be decomposed further by subsequent<br />
heat treatment of the irradiated polymer, resulting in crosslinking<br />
of UHMWPE chains in the region of the material near the surface. As<br />
a result of this surface modification, the surface hardness of UHMWPE<br />
substantially increases.<br />
18.5.2 Grafting onto Poly(tetrafluoroethylene)<br />
18.5.2.1 Diazonium Salts<br />
Functionalization of poly(tetrafluoroethylene) (PTFE) surfaces can be<br />
achieved by diazonium salts. Reduced PTFE can be grafted by nitro <strong>and</strong><br />
bromophenyldiazonium tetrafluoroborate salts in a manner similar to that<br />
used for carbon, except that no application of a reductive potential during<br />
grafting is required. The grafting is evidenced by cyclic voltametry, X-<br />
ray fluorescence or time of flight single ion monitoring mass spectroscopy<br />
(TOF-SIMS). 100–102<br />
18.5.2.2 Epoxide-containing Monomers<br />
A pretreated PTFE film with argon plasma can be further modified by<br />
a graft copolymerization with hydrophilic <strong>and</strong> epoxide-containing monomers.<br />
The grafting is initiated by UV light. Functional monomers for<br />
grafting include acrylic acid (AA), sodium salt of p-styrenesulfonic acid,<br />
N,N-dimethylacrylamide (DMAA), <strong>and</strong> glycidyl methacrylate (GMA).<br />
A stratified surface microstructure with a significantly higher ratio<br />
of substrate to grafted chains in the top surface layer than in the subsurface<br />
layer is always obtained. The grafted PTFE films show a number of new<br />
issues. These include: 103<br />
• Covalent immobilization of an enzyme, such as trypsin, for AA<br />
graft copolymerized surface,<br />
• Change transfer included coating of an electroactive polymer, such<br />
as polyaniline, for AA <strong>and</strong> styrenesulfonic acid graft copolymerized<br />
surfaces,
648 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
• Adhesive-free adhesion between two PTFE surfaces, for AA, styrenesulfonic<br />
acid <strong>and</strong> DMAA graft copolymerized surfaces,<br />
• Improved adhesive bonding via interfacial crosslinking of the<br />
grafted chains, for GMA graft copolymerized surfaces.<br />
18.5.2.3 2-Hydroxyethyl acrylate<br />
Surface modifications of Ar plasma pretreated poly(tetrafluoroethylene)<br />
(PTFE) film via graft copolymerization improve the adhesion of copper.<br />
The PTFE film surface is initially modified by graft copolymerization<br />
with a monomer, such as 2-hydroxyethyl acrylate <strong>and</strong> acrylamide.<br />
These monomers contain the functional groups for epoxide groups. The<br />
modified PTFE surface is subsequently again exposed to an Ar plasma <strong>and</strong><br />
subjected to UV induced graft copolymerization with glycidyl methacrylate.<br />
104<br />
18.5.2.4 Glycidyl Methacrylate<br />
The surface modification of a PTFE film is done by the deposition of glycidyl<br />
methacrylate (GMA) in the presence of H 2 plasma activation of the<br />
PTFE substrates. The H 2 plasma treatment results in an effective defluorination<br />
<strong>and</strong> hydrogenation of the PTFE surface. This enhances the adhesion<br />
of Cu vapor onto the PTFE surface.<br />
In addition, a plasma polymerization with glycidyl methacrylate is<br />
performed. High adhesion strength for the Cu on such a surface is obtained<br />
only in the presence of H 2 plasma activation of the PTFE substrates prior<br />
to the plasma polymerization <strong>and</strong> deposition of GMA. In the absence of<br />
H 2 plasma pre-activation, the deposited pp-GMA layer on the PTFE surface<br />
can be readily removed by acetone extraction. The enhancement of<br />
the adhesion of the Cu on the surface is attributed to the covalent bonding<br />
of the pp-GMA layer with the PTFE surface, the preservation of the epoxide<br />
functional groups in the pp-GMA layer, <strong>and</strong> the strong interaction of<br />
evaporated Cu atoms with the epoxide <strong>and</strong> carboxyl groups of the GMA<br />
chains. 105<br />
18.5.2.5 Oxygen <strong>and</strong> Ammonia Plasmas<br />
PTFE can be treated in oxygen or ammonia plasmas in order to introduce<br />
oxygen-containing or nitrogen-containing groups, respectively. These
Grafting 649<br />
groups increase the surface free energy <strong>and</strong> allow the adsorption of polyelectrolytes<br />
via electrostatic interactions. 106 The effects of such a modification<br />
can be evaluated by means of contact angle measurements.<br />
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5(1):238–244, January–February 2004.<br />
73. N. Sombatsompop, K. Sungsanit, <strong>and</strong> C. Thongpin. Structural changes of<br />
pvc in pvc/LDPE melt-blends: Effects of LDPE content <strong>and</strong> number of<br />
extrusions. Polym. Eng. Sci., 44(3):487–495, March 2004.<br />
74. X.-M. Xie <strong>and</strong> X. Zheng. Effect of addition of multifunctional monomers<br />
on one-step reactive extrusion of PP/PS blends. Materials & Design, 22(1):<br />
11–14, February 2001.<br />
75. V. M. Hoo, R. A. Whitney, <strong>and</strong> W. E. Baker. Free-radical grafting of<br />
co-monomer systems onto an ester-containing polymer. Polymer, 41(11):<br />
4367–4371, May 2000.<br />
76. W. Jarowenko. Acetylated starch <strong>and</strong> miscellaneous organic esters. In O. B.<br />
Wurzburg, editor, Modified Starches: Properties <strong>and</strong> Uses, chapter 4, pages<br />
55–78. CRC Press, Inc., Boca Raton, FL, 1986.<br />
77. N. Gimmler, F. Lawn, <strong>and</strong> F. Meuser. Influence of extrusion cooking conditions<br />
on the efficiency of the cationization <strong>and</strong> carboxymethylation of potato<br />
starch granules. Starch, 46:268–276, 1994.<br />
78. Y. H. Chang <strong>and</strong> C. Y. Lii. Preparation of starch phosphates by extrusion.<br />
J. Food Sci., 57:203–205, 1992.<br />
79. P. Tomasik, Y. J. Wang, <strong>and</strong> J. L. Jane. Facile route to anionic starches. succinylation,<br />
maleination <strong>and</strong> phthalation of corn starch on extrusion. Starch,<br />
47:96–99, 1995.<br />
80. R. E. Wing <strong>and</strong> J. L. Willett. Water soluble oxidized starches by reactive<br />
extrusion. Industrial Crops <strong>and</strong> Products, 7:45–52, 1997.
Grafting 655<br />
81. V. D. Miladinov <strong>and</strong> M. A. Hanna. Starch esterification by reactive extrusion.<br />
Industrial Crops <strong>and</strong> Products, 11(1):51–57, January 2000.<br />
82. J. L. Willett <strong>and</strong> V. L. Finkenstadt. Preparation of starch-graft-polyacrylamide<br />
copolymers by reactive extrusion. Polym. Eng. Sci., 43(10):1666–1674,<br />
October 2003.<br />
83. L. K. Børve <strong>and</strong> H. K. Kotlar. Preparation of high viscosity thermoplastic<br />
phenol formaldehyde polymers for application in reactive extrusion. Polymer,<br />
39(26):6921–6927, December 1998.<br />
84. T. Shimizu, S. Higashiura, M. Wada, H. Tanaka, <strong>and</strong> M. Ohguchi. Grafting<br />
reaction product <strong>and</strong> method for producing the same. US Patent 5 656 681,<br />
assigned to Toyo Boseki Kabushiki Kaisha (Osaka, JP), August 12 1997.<br />
85. G. S. S. Rao <strong>and</strong> R. C. Jain. Graft copolymerisation of N-vinyl pyrrolidone<br />
onto polypropylene copolymer in melt: Effect of grafting thermomechanical<br />
properties <strong>and</strong> paint adhesion. J. Appl. Polym. Sci., 88(9):2173–2180,<br />
May 2003.<br />
86. M. Husemann <strong>and</strong> S. Zöllner. Processing of acrylic hotmelts by reactive<br />
extrusion. US Patent 6 753 079, assigned to Tesa AG (Hamburg, DE), June<br />
22 2004.<br />
87. B. C. Trivedi <strong>and</strong> B. M. Culbertson. Maleic Anhydride. Plenum Press, New<br />
York, 1982.<br />
88. M. R. Thompson, C. Tzoganakis, <strong>and</strong> G. L. Rempel. Terminal functionalization<br />
of polypropylene via the alder ene reaction. Polymer, 39(2):<br />
327–334, 1998.<br />
89. E. Kim, E. Lee, I. Park, <strong>and</strong> T. Chang. End functionalization of styrenebutadiene<br />
rubber with poly(ethylene glycol)-poly(dimethylsiloxane) terminator.<br />
Polym. J., 34(9):674–681, 2002.<br />
90. M. F. Farona. Benzocyclobutenes in polymer chemistry. Prog. Polym. Sci.,<br />
21(3):505–555, 1996.<br />
91. T. Kavc, W. Kern, M. F. Ebel, R. Svagera, <strong>and</strong> P. Polt. Surface modification<br />
of polyethylene by photochemical introduction of sulfonic acid groups.<br />
Chem. Mat., 12(4):1053–1059, April 2000.<br />
92. J. P. Lens, J. G. A. Terlingen, G. H. M. Engbers, <strong>and</strong> J. Feijen. Introduction<br />
of sulfate groups on poly(ethylene) surfaces by argon plasma immobilization<br />
of sodium alkyl sulfates. Polymer, 39(15):3437–3444, July 1998.<br />
93. S. Balamurugan, A. B. M<strong>and</strong>ale, S. Badrinarayanan, <strong>and</strong> S. P. Vernekar.<br />
Photochemical bromination of polyolefin surfaces. Polymer, 42(6):<br />
2501–2512, March 2001.<br />
94. N. Chanunpanich, A. Ulman, Y. M. Strzhemechny, S. A. Schwarz, J. Dormicik,<br />
A. Janke, H. G. Braun, <strong>and</strong> T. Kratzmuller. Grafting polythiophene on<br />
polyethylene surfaces. Polym. Int., 52(1):172–178, January 2003.<br />
95. V. Svorcik, V. Rybka, I. Stibor, V. Hnatowicz, J. Vacik, <strong>and</strong> P. Stopka. Synthesis<br />
of grafted polyethylene by ion beam modification. Polym. Degrad.<br />
Stabil., 58(1-2):143–147, 1997.
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96. J. X. Lei, J. Gao, R. Zhou, B. S. Zhang, <strong>and</strong> J. Wang. Photografting of<br />
acrylic acid on high density polyethylene powder in vapour phase. Polym.<br />
Int., 49(11):1492–1495, November 2000.<br />
97. H. Fujimatsu, M. Imaizumi, N. Shibutani, H. Usami, <strong>and</strong> T. Iijima. Modification<br />
of high-strength <strong>and</strong> high-modulus polyethylene fiber surfaces for<br />
the purpose of dyeing. Polym. J., 33(7):509–513, 2001.<br />
98. M. Li, J. X. Lei, J. Gao, <strong>and</strong> Z. J. Su. Surface graft copolymerization of<br />
hydrogen silicone fluid onto low density polyethylene film through corona<br />
discharge <strong>and</strong> the properties of grafted film. Polym.-Plast. Technol. Eng.,<br />
42(2):207–215, 2003.<br />
99. O. N. Tretinnikov, S. Ogata, <strong>and</strong> Y. Ikada. Surface crosslinking of polyethylene<br />
by electron beam irradiation in air. Polymer, 39(24):6115–6120,<br />
November 1998.<br />
100. C. Combellas, F. Kanoufi, D. Mazouzi, A. Thiebault, P. Bertr<strong>and</strong>, <strong>and</strong><br />
N. Medard. Surface modification of halogenated polymers. 4. functionalisation<br />
of poly(tetrafluoroethylene) surfaces by diazonium salts. Polymer,<br />
44(1):19–24, January 2003.<br />
101. C. Combellas, F. Kanoufi, D. Mazouzi, <strong>and</strong> A. Thiebault. Surface modification<br />
of halogenated polymers: 5. localized electroless deposition of metals<br />
on poly(tetrafluoroethylene) surfaces. J. Electroanal. Chem., 556:43–52,<br />
September 2003.<br />
102. C. Combellas, A. Fuchs, F. Kanoufi, D. Mazouzi, <strong>and</strong> S. Nunige. Surface<br />
modification of halogenated polymers. 6. graft copolymerization of<br />
poly(tetrafluoroethylene) surfaces by polyacrylic acid. Polymer, 45(14):<br />
4669–4675, June 2004.<br />
103. E. T. Kang, K. G. Neoh, K. L. Tan, B. C. Senn, P. J. Pigram, <strong>and</strong><br />
J. Liesegang. Surface modification <strong>and</strong> functionalization of polytetrafluoroethylene<br />
films via graft copolymerization. Polym. Adv. Technol., 8(11):<br />
683–692, November 1997.<br />
104. S. Y. Wu, E. T. Kang, K. G. Neoh, <strong>and</strong> K. L. Tan. Surface modification<br />
of poly(tetrafluoroethylene) films by double graft copolymerization for adhesion<br />
improvement with evaporated copper. Polymer, 40(25):6955–6964,<br />
December 1999.<br />
105. X. P. Zou, E. T. Kang, K. G. Neoh, C. Q. Cui, <strong>and</strong> T. B. Lim. Surface<br />
modification of poly(tetrafluoroethylene) films by plasma polymerization<br />
of glycidyl methacrylate for adhesion enhancement with evaporated copper.<br />
Polymer, 42(15):6409–6418, July 2001.<br />
106. U. Lappan, H. M. Buchhammer, <strong>and</strong> K. Lunkwitz. Surface modification of<br />
poly(tetrafluoroethylene) by plasma pretreatment <strong>and</strong> adsorption of polyelectrolytes.<br />
Polymer, 40(14):4087–4091, June 1999.
19<br />
Acrylic Dental Fillers<br />
<strong>Polymers</strong> in dental applications are used as restorative materials, cements,<br />
adhesives, cavity liners, <strong>and</strong> as protective sealants for pits <strong>and</strong> fissures. The<br />
use of composite resins is recommended for amalgam replacement.<br />
<strong>Polymers</strong> are further used as denture base materials, denture relines,<br />
crown <strong>and</strong> bridge resins, dental impressions, <strong>and</strong> duplicating materials.<br />
There are monographs on the topic. 1–5<br />
Polymeric materials used in dental applications must meet certain<br />
physical, chemical, biological, <strong>and</strong> aesthetic requirements. These requirements<br />
include<br />
• Adequate strength<br />
• Resilience,<br />
• Abrasion resistance,<br />
• Dimensional stability,<br />
• Color stability,<br />
• Resistance to body fluids,<br />
• Tissue tolerance, low allergenicity, toxicity, mutagenicity, carcinogenic<br />
responses.<br />
Further, the materials should be easy to use <strong>and</strong> should not be expensive.<br />
657
658 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
19.1 HISTORY<br />
The first polymeric materials used in dental applications were guttapercha,<br />
celluloid, phenol/formaldehyde, <strong>and</strong> acrylic resins. <strong>Polymers</strong> such<br />
as acrylics, poly(styrene)s, poly(carbonate)s, <strong>and</strong> polysulfones can be injection-molded<br />
to yield dentures with outst<strong>and</strong>ing toughness, high fatigue<br />
strength, <strong>and</strong> low water absorption. Most common are acrylic-based resins.<br />
However, other classes also gain importance, such as spiro orthocarbonates,<br />
cycloaliphatic epoxy compounds, cyclic ketene acetals <strong>and</strong> 2-vinylcyclopropanes,<br />
5, 6 because of the dem<strong>and</strong> for low shrinkage materials. Often<br />
these monomers are in combination with acrylic-based resins. We will<br />
mention these classes briefly here.<br />
Acrylic resins have been used in the construction of denture bases<br />
since 1930. 4 Multifunctional acrylates <strong>and</strong> methacrylates can be polymerized<br />
to crosslinked polymers to be used as restorative materials. A<br />
polymerization involving cold curing is carried out with redox initiators at<br />
ambient temperature.<br />
Bisphenol A diglycidyl ether dimethacrylate with a ceramic filler<br />
opened a new area in the state of the art. A silane coupling agent between<br />
ceramics <strong>and</strong> organic polymer increases the adhesion strength.<br />
The principle of photopolymerization for dental resins was introduced<br />
around 1975. Also, a polyurethane resin, based on polyurethane<br />
dimethacrylate <strong>and</strong> similar monomers was developed 7 that can be cured<br />
with visible light.<br />
19.2 POLYMERIC COMPOSITE FILLING MATERIALS<br />
An overview of the ingredients in a dental composite is given in Table 19.1.<br />
Dental polymeric composite filling materials consist of di- <strong>and</strong> trifunctional<br />
monomer systems that undergo crosslinking in the course of<br />
polymerization. Reinforcing fillers are silanized quartz, glass, <strong>and</strong> ceramics.<br />
The polymerization must be initialized effectively under oral conditions.<br />
Various additives may increase the chemical stability of the cured<br />
materials. Dental sealants mostly are not filled with reinforcing fillers.<br />
Dental composites may be used as two-component formulations or as a<br />
one-component formulation.
Acrylic Dental Fillers 659<br />
Table 19.1: Constituents in a Dental Composite<br />
Compound Type<br />
Organic resin<br />
Initiator systems<br />
Polymerization inhibitors<br />
Fillers<br />
Pigments<br />
Coloring or tint agents<br />
Caries inhibiting agents<br />
Fluoride release agents<br />
UV-absorbers<br />
Stabilizers<br />
Surfactants<br />
Thickening agents<br />
19.3 MONOMERS<br />
Common monomers are shown in Table 19.2. Some acrylics <strong>and</strong> methacrylics<br />
are shown in Figure 19.1.<br />
19.3.1 Acrylics <strong>and</strong> Methacrylics<br />
Most common thermosets are methacrylate based, for example, 2,2-bis[p-<br />
(2-hydroxy-3-methacryloxypropoxy)phenyl]propane, i.e., the bisphenol A<br />
adduct of glycidylmethacrylate (Bis-GMA) <strong>and</strong> triethylene glycol dimethacrylate<br />
(TEGDMA), c.f. Figure 19.1.<br />
19.3.1.1 Urethane-modified Acrylics<br />
The reaction product of 1,6-hexamethylenediisocyanate <strong>and</strong> ethylene glycoldimethacrylate<br />
or other glycol esters is also a suitable monomer. Other<br />
urethane dimethacrylates are 1,6-bis(methacryloxy-2-ethoxycarbonylamino)-2,4,4-trimethylhexane<br />
(UDMA). Further polyurethane dimethacrylate<br />
(PUDMA) is commonly used as a principal polymer in dental restoratives<br />
of this type.<br />
Urethane derivatives of Bis-GMA exhibit lower viscosities <strong>and</strong> are<br />
more hydrophobic than Bis-GMA. In general, the viscosities of these<br />
monomers decrease with increasing chain length of the alkyl urethane substituent.<br />
Since Bis-GMA, PUDMA, <strong>and</strong> others are still highly viscous at
660 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Vinyl Monomer<br />
Table 19.2: Monomers for Dental <strong>Polymers</strong><br />
Reference<br />
2,2-Bis[4-(3-methacryloxy-2-hydroxypropoxy)phenyl]propane<br />
(Bis-GMA)<br />
Bisphenol A dimethacrylate (Bis-A-Dima)<br />
Ethoxylated Bis-A-Dima<br />
Triethylene glycol dimethacrylate (TEGDMA)<br />
Ethoxylated bisphenol A dimethacrylate (EBPDMA)<br />
Hydroxyethyl methacrylate (HEMA)<br />
Hydroxyethyl methacrylate maleic anhydride adduct (HEMAN)<br />
8<br />
1,1,1-Trimethylolpropane trimethacrylate (TMPTMA)<br />
Tetrahydrofurfuryl cyclohexene dimethacrylate (TCDM)<br />
Hexafunctional methacrylate ester (HME)<br />
1,6-Hexanediol dimethacrylate (HDDMA)<br />
9<br />
2-Isocyanatoethyl methacrylate (IEM)<br />
10<br />
Di-2-methacryloxyethyl-2,2,4-trimethylhexamethylene<br />
dicarbamate (UDMA)<br />
Polyurethane dimethacrylate (PUDMA) esters<br />
Tetrahydrofurfuryl methacrylate (THFMA)<br />
Glycidyl methacrylate (GMA)<br />
Methacryloyl-β-alanine (MBA)<br />
11<br />
Methacryloyl glutamic acid<br />
11<br />
Acryloyl-β-alanine<br />
11<br />
Acryloyl glutamic acid<br />
11<br />
Poly(carbonate)dimethacrylate (PCDMA)<br />
12<br />
Cyclic Monomers<br />
Reference<br />
α-Methylene-γ-butyrolactone<br />
13<br />
Epoxy Monomers<br />
Reference<br />
Cycloaliphatic diepoxide<br />
14<br />
Epoxylated vinyl ether<br />
14
Acrylic Dental Fillers 661<br />
OH<br />
CH 3<br />
OH<br />
CH CH 2<br />
C<br />
CH 2 CH<br />
CH 2 CH 3 CH 2<br />
O<br />
C<br />
C<br />
O<br />
CH 3<br />
O<br />
H 3 C<br />
CH 2 CH 2<br />
CH 2<br />
CH2<br />
O<br />
O<br />
CH 2<br />
CH2<br />
Bis-GMA<br />
CH 2<br />
O<br />
CH2<br />
O<br />
TEGDMA<br />
O<br />
C<br />
C<br />
O<br />
CH 3<br />
CH 2 C<br />
C CH 2<br />
CH 3<br />
O<br />
C<br />
C<br />
CH 2<br />
CH 3<br />
C C<br />
O<br />
O CH 2 CH 2 OH<br />
HEMA<br />
CH 2<br />
CH 3<br />
C C<br />
O<br />
O CH 2<br />
O<br />
THFMA<br />
CH 2<br />
CH 3<br />
C C<br />
O<br />
O CH 2 CH 2 N C O<br />
IEM<br />
CH 2<br />
CH 3<br />
C C<br />
O<br />
O CH 2 CH 2<br />
O<br />
GMA<br />
Figure 19.1: 2,2-Bis[p-(2-hydroxy-3-methacryloxypropoxy)phenyl]propane<br />
(Bis-GMA), Triethylene glycol dimethacrylate (TEGDMA), Hydroxyethyl methacrylate<br />
(HEMA), Tetrahydrofurfuryl methacrylate (THFMA), 2-Isocyanatoethyl<br />
methacrylate (IEM), Glycidyl methacrylate (GMA)
662 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 19.3: Example for a Resin Matrix 9<br />
Monomers %<br />
Ethoxylated bisphenol A dimethacrylate 30<br />
Polyurethane dimethacrylate ester 50<br />
1,6-Hexanediol dimethacrylate 20<br />
Initiator System<br />
phr<br />
Camphorquinone 0.1<br />
Ethyl-4-dimethylamino benzoate 0.3<br />
2,4,6-Trimethylbenzoyldiphenylphosphine oxide 0.2<br />
room temperature, they are generally diluted with an acrylate or methacrylate<br />
monomer having a lower viscosity, such as trimethylolpropyl trimethacrylate,<br />
1,6-hexanediol dimethacrylate, or 1,3-butanediol dimethacrylate.<br />
Other dimethacrylate monomers, such as ethylene glycol dimethacrylate,<br />
diethylene glycol dimethacrylate, triethylene glycol dimethacrylate, poly-<br />
(ethylene glycol)dimethacrylate (PEGDMA) <strong>and</strong> tetraethylene glycol dimethacrylate,<br />
are also in general use as diluents. 7<br />
The photopolymerization of these monomers shows high degrees<br />
of conversion of the vinyl groups in comparison to Bis-GMA. <strong>Polymers</strong><br />
with lower polymerization shrinkages at equivalent degrees of vinyl conversion<br />
than Bis-GMA are obtained. The refractive indices of the urethane<br />
derivatives were similar to Bis-GMA. However the flexural strengths of<br />
the polymers are lower than that of the Bis-GMA homopolymer. The flexural<br />
strengths decrease with increasing chain length of the alkyl urethane<br />
substituent. 15 An example for a resin matrix is shown in Table 19.3.<br />
19.3.1.2 Isocyanatomethacrylates<br />
The potential utility of isocyanatomethacrylates in dental adhesives arises<br />
from the possibility of dual modes of reaction, i.e., free-radical polymerization<br />
via the methacrylate double bonds, <strong>and</strong> the reaction via the NCO<br />
group with active hydrogens in a suitable compound to be admixed. 10<br />
19.3.1.3 Nematic Acrylics<br />
Zero polymerization shrinkage is one of the most necessary features of a<br />
dental restorative so that accumulated stresses do not debond the dentinrestorative<br />
interface or fracture the tooth or restorative which can result in
Acrylic Dental Fillers 663<br />
marginal leakage <strong>and</strong> microbial attack. This feature is also important in<br />
bone repair <strong>and</strong> in accurate reproduction of photolithographic imprints <strong>and</strong><br />
optical elements.<br />
Attempts have been made to reduce polymerization shrinkage by utilizing<br />
nematic liquid crystal monomers. The expected low polymerization<br />
shrinkage for such compounds originates from the high packing efficiency<br />
that already exists in the nematic state, thus minimizing the entropy reduction<br />
that occurs during polymerization. Liquid crystal monomers or<br />
prepolymers have another advantage in that the viscosity is lower than that<br />
of an isotropic material of the same molecular weight. 16<br />
An example for a liquid crystalline methacrylate is shown in Figure<br />
19.2, i.e. 4,4 ′ -Bis(2-hydroxy-3-methacryloylpropoxy)biphenyl esterified<br />
with 4 ′ -cyano-4-biphenyloxyvaleric acid. The liquid crystalline di(meth)-<br />
acrylate is synthesized by the reaction of 2,3-epoxypropoxy methacrylate<br />
with 4,4 ′ -dihydroxybiphenyl to form a methacrylate-terminated macromonomer<br />
having hydroxyl groups. The macromonomer hydroxyl groups<br />
are then esterified with 4 ′ -cyano-4-biphenyloxyvaleric acid. The (meth)-<br />
acrylate polymerizes quantitatively <strong>and</strong> with very low volume shrinkage of<br />
less than 2.5%. 17<br />
19.3.1.4 Amino Acid Derivatives of Acrylics<br />
It is known that unreacted 2-hydroxyethyl methacrylate (HEMA) in current<br />
resin-modified glass ionomer cements (RMGICs) shows potential cytotoxicity<br />
to pulp <strong>and</strong> surrounding tissues. 18 Amino acid acrylate <strong>and</strong> methacrylate<br />
derivatives were found to be suitable in light curable glass-ionomer cements<br />
(LCGIC). Methacryloyl <strong>and</strong> acryloyl derivatives of the amino acids<br />
can be synthesized via the Schotten-Baumann reaction.<br />
Among several derivatives, methacryloyl-β-alanine (MBA) has a<br />
particularly low solution viscosity <strong>and</strong> a high compressive strength. The<br />
LCGIC system based on amino acid derivatives is free from HEMA.<br />
This system may eliminate a potential cytotoxicity in LCGICs caused by<br />
leached HEMA. Optimal MBA-modified cements are higher in certain mechanical<br />
properties in comparison to conventional cements. 11<br />
19.3.1.5 Phosphoric Esters<br />
Phosphoric acid esters with pendant acrylate or methacrylate functions<br />
serve as adhesion promoters to fillers such as surface active glasses. Ex-
664 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
CH 2 CH 2<br />
CH CH 3<br />
H 3 C<br />
C O O<br />
O<br />
CH<br />
C<br />
O<br />
CH 2<br />
HC H 2 C<br />
O<br />
C O<br />
O O CH 2<br />
O<br />
CH 2<br />
CH<br />
O<br />
C<br />
CH 2<br />
CH 2<br />
CH 2<br />
CH 2<br />
CH 2<br />
CH 2<br />
CH 2 CH 2<br />
O<br />
O<br />
C<br />
N<br />
C<br />
N<br />
Figure 19.2: Nematic Monomer, 4,4 ′ -Bis(2-hydroxy-3-methacryloylpropoxy)biphenyl<br />
esterified with 4 ′ -cyano-4-biphenyloxyvaleric acid17, 19
Acrylic Dental Fillers 665<br />
amples are 2-(methacryloyloxy)ethyl phosphate, bis[2-(methacryloyloxy)-<br />
ethyl]phosphate 7 or pentaerythritol trimethacrylate monophosphate. They<br />
added up to 5% with respect to the organic curable composition.<br />
19.3.1.6 Hydrophobic-Modified Acrylics<br />
Hydrophobic composites stronger than methacrylate prepolymers, are the<br />
corresponding analogues where most of the hydrogens are replaced by fluorine.<br />
19.3.2 Cyclic Monomers<br />
Cyclic monomers generally exhibit less shrinkage in the course of polymerization<br />
as the polymerization process occurs by a ring opening reaction,<br />
in contrast to vinyl monomer that is basically the ring opening of a<br />
two membered ring, i.e., the double bond.<br />
α-Methylene-γ-butyrolactone (MBL) is an exp<strong>and</strong>ing monomer <strong>and</strong><br />
does not cause shrinkage of the material during polymerization. It can<br />
be described as the cyclic analog of methyl methacrylate, <strong>and</strong> it exhibits<br />
greater reactivity in free-radical polymerization than conventional methacrylate<br />
monomers. 13<br />
19.3.2.1 Spiroorthocarbonates<br />
Spiroorthocarbonates (SOC), spiroorthoesters (SOE) <strong>and</strong> bicyclic orthoesters<br />
are attractive because they show a very low shrinkage or even expansion<br />
during polymerization. 20, 21 Spiroorthocarbonates with polymerizable<br />
double bonds have been investigated; some of them are shown in Figure<br />
19.3. A few are bearing methacrylic substructures. 21<br />
Spiroorthocarbonates with seven membered rings show a high tendency<br />
of ring opening when they undergo a radical polymerization. This is<br />
favorable for low shrinkage. Spiroorthocarbonate compounds that include<br />
epoxy groups as a substituent have been described. 22<br />
The synthesis of 7,26-Dioxatrispirobicyclo[4.1.0]heptane-4,5 ′ -1,3-dioxane-2<br />
′ ,2 ′′ -1,3-dioxane-5 ′′ ,4 ′′ -bicyclo[4.1.0]heptane (DCHE) is shown<br />
in Figure 19.4. It has been concluded that although the polymerization<br />
shrinkage has been one of the main shortcomings of resin-based composites,<br />
the ring-opening polymerization of cyclic monomers has not been successfully<br />
achieved for commercial dental filling materials. 5
666 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O O<br />
O<br />
O<br />
Figure 19.3: Spiroorthocarbonates with Polymerizable Double Bonds 21<br />
19.3.3 Epoxy Monomers<br />
Acrylate based compositions have the disadvantage of shrinking strongly<br />
at hardening. Epoxy compounds containing compositions are known; they<br />
can undergo cationic polymerization with low shrinkage. In this case, it is<br />
necessary to use a high energy light source for such a polymerization, e.g.,<br />
a mercury vapor lamp, which cannot be used in medical practices because<br />
of the danger of combustion. Certain compositions are not completely<br />
cured <strong>and</strong> do not fulfill the requirements of adhesiveness <strong>and</strong> abrasiveness.<br />
To achieve a complete hardening, it is necessary to apply a thermic aftertreatment,<br />
which is not practicable in the mouth of a patient. 14<br />
However, a composition obtained by the combination of a cyclic<br />
diepoxide, tetrahydrofuran, diphenyliodoniumhexafluorantimonate <strong>and</strong><br />
camphorquinone by means of accelerators, e.g., 4-dimethylaminobenzaldehyde,<br />
4-dimethylaminophenethanol, dihydroxyethyl-p-toluidine, ethyl-<br />
4-dimethylamino benzoate can be cured at wavelengths of 400 to 1000<br />
nm. These materials can be used in dental applications. 23<br />
N,N-bis-hydroxyalkyl-p-aminobenzoic acid alkyl esters have an excellent<br />
efficiency as accelerators of the light induced hardening of a composition<br />
based on epoxy compounds. 14
Acrylic Dental Fillers 667<br />
OH<br />
+<br />
OH<br />
O<br />
Bu<br />
Sn<br />
Bu<br />
S<br />
Cl<br />
C<br />
Cl<br />
+<br />
HO<br />
HO<br />
O Bu<br />
Sn<br />
O Bu<br />
+<br />
S<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
O<br />
Figure 19.4: Synthesis of 7,26-Dioxatrispirobicyclo[4.1.0]heptane-4,5 ′ -1,3-dioxane-2<br />
′ ,2 ′′ -1,3-dioxane-5 ′′ ,4 ′′ -bicyclo[4.1.0]heptane (DCHE) 22
668 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Catalyst<br />
Table 19.4: Chemical Curing Systems24, 25<br />
Dibenzoyl peroxide<br />
Organic peroxides<br />
Hydroperoxides<br />
Peroxides<br />
Barbituric acid<br />
Aryl borate<br />
Tri-n-butylborane<br />
Promoter<br />
Tertiary aromatic amines<br />
4-(N,N-Dimethylamino)phenethyl alcohol 26<br />
Cobalt salt<br />
Thioureas<br />
Ascorbic acid<br />
Cu 2+ Cl-compound<br />
Acid<br />
Oxygen<br />
19.3.4 Highly Loaded Composite<br />
In general, a highly loaded composite looks very dry <strong>and</strong> is hard to h<strong>and</strong>le.<br />
Suitable monofunctional monomers may be used to act as a diluent<br />
to control or reduce the viscosity of the resin as well as to provide fewer<br />
polymerization sites, both of which assist in formulating the composition.<br />
The addition of a viscosity controlling monofunctional monomer makes<br />
the composition <strong>and</strong> composites easier to h<strong>and</strong>le.<br />
19.4 RADICAL POLYMERIZATION<br />
Initiators for methacrylics generally fall within one of three categories:<br />
1. Cold curing chemical systems that initiate polymerization upon<br />
admixing two or more compounds,<br />
2. light initiated initiator systems,<br />
3. heat initiated initiator systems.<br />
19.4.1 Chemical Curing Systems<br />
Cold curing chemical systems include traditional free-radical polymerization<br />
initiators normally used with polymerizable ethylenically unsaturated<br />
materials <strong>and</strong> resins.<br />
A variety of catalysts for chemical polymerization have been proposed.<br />
The types of chemical curing systems are summarized in Table 19.4.
Acrylic Dental Fillers 669<br />
19.4.1.1 Peroxide Amine Systems<br />
For example, organic peroxide initiators <strong>and</strong> amine accelerations may be<br />
used. The initiators are admixed with the monomers shortly before application<br />
to the tooth or dental appliance. 25 The kinetics of curing of several<br />
dimethacrylate monomers initiated by a dibenzoyl peroxide amine system<br />
has been studied using differential scanning calorimetry. 26 A mathematical<br />
model was developed to describe the rate of polymerization.<br />
Here tertiary amines are aromatic tertiary amines, for example,<br />
ethyl-4-dimethylamino benzoate (EDMAB), 2-[4-(dimethylamino)phenyl]<br />
ethanol, N,N-dimethyl-p-toluidine (DMPT), bis(hydroxyethyl)-p-toluidine,<br />
<strong>and</strong> triethanolamine. Such accelerators are generally present in the<br />
range from about 0.5 to about 4.0% of the resin composition. 9<br />
The combination of the organic peroxide <strong>and</strong> the tertiary amine involves<br />
problems such as tinting the cured product due to oxidation of the<br />
amine compound <strong>and</strong> discoloration, <strong>and</strong> impairing the polymerization due<br />
to oxygen <strong>and</strong> acidic components. An acidic component would produce a<br />
quaternary salt which does not exhibit reducing ability upon reacting with<br />
the tertiary amine.<br />
The problem of tinting or discoloration causes the color tone to differ<br />
from that of a natural tooth when the catalyst is used for a dental restorative<br />
as represented by a composite resin, <strong>and</strong> deteriorates the aesthetic value.<br />
Impairing the polymerization means that the catalyst cannot be used for the<br />
dental adhesive that uses an acid group-containing polymerizable monomer<br />
as an essential component. 24<br />
19.4.1.2 Hydroperoxides Thiourea Systems<br />
Other redox initiators are hydroperoxides with thioureas, <strong>and</strong> peroxides<br />
with ascorbic acid. A two-part system may be built up as follows: One part<br />
contains an initiator. The second part comprises filler <strong>and</strong> the co-initiator.<br />
The two parts are spatuled (mixed) to form a cement prior to placement on<br />
tooth.<br />
19.4.1.3 Barbituric Acid-based Initiators<br />
Catalyst systems based on barbituric acid are most generally used in the<br />
field of dental materials because of relatively low harmful effect on the<br />
body <strong>and</strong> ready availability. 1-benzyl-5-phenylbarbituric acid can be used
670 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Bu<br />
B<br />
Bu<br />
O 2<br />
Bu<br />
O<br />
O<br />
B<br />
Bu<br />
Bu<br />
Bu<br />
Bu<br />
Bu<br />
B<br />
Bu O<br />
Bu<br />
O<br />
Bu<br />
B<br />
Bu<br />
*O<br />
Bu<br />
Bu<br />
B<br />
Bu<br />
Bu<br />
B O* Bu<br />
Bu<br />
Bu = CH 3 CH 2 CH 2 CH 2<br />
Bu<br />
O<br />
Bu<br />
B<br />
Bu<br />
Bu*<br />
Figure 19.5: Radical Generating Mechanisms of Alkylboranes 27<br />
in combination with peroxide <strong>and</strong> with a heavy metal accelerator in a second<br />
component. 28 However, a barbituric acid-type catalyst can cause problems,<br />
such as the difficulty in controlling the curing time <strong>and</strong> poor preservation<br />
stability.<br />
24, 29<br />
19.4.1.4 Borane <strong>and</strong> Borate-based Initiators<br />
Triethylborane initiates a very fast polymerization of methyl methacrylate.<br />
Since some radical inhibitors are active in the inhibition, the type of<br />
polymerization was identified as a radical polymerization. In a series of experiments,<br />
high molecular weight polymers were produced in the presence<br />
of p-benzoquinone. Consequently a speculative mechanism was postulated<br />
that an adduct of quinone <strong>and</strong> borane should be responsible for the<br />
initiation. 30 The basic radical generating mechanism of borane systems is<br />
shown in Figure 19.5. Trialkylborane or the partial oxide thereof is an excellent<br />
promoter for chemical polymerization <strong>and</strong> is very active, but it is<br />
chemically unstable. Therefore, this catalyst must be packaged separately<br />
from other components, must be picked up in suitable amounts just before
Acrylic Dental Fillers 671<br />
it is used <strong>and</strong> must be mixed with other monomer components, requiring<br />
cumbersome operation, which is a drawback.<br />
Aryl borate as catalyst is easy to h<strong>and</strong>le, does not cause the cured<br />
product to be tinted or discolored, <strong>and</strong> exhibits excellent preservation stability<br />
without, however, exhibiting sufficient activity for polymerization.<br />
The activity for polymerization is greatly enhanced when an aryl<br />
borate compound <strong>and</strong> an acidic compound are used in combination with a<br />
particular oxidizing agent.<br />
Suitable peroxides are methylethylketone peroxide, cumene hydroperoxide<br />
or tert-hexyl hydroperoxide. A mixture of 2-methacryloyloxyethyldihydrogen<br />
phosphate <strong>and</strong> bis(2-methacryloyloxyethyl)hydrogen phosphate<br />
is used as acidic compound. Optional metal compounds are ferric<br />
acetylacetonate <strong>and</strong> copper(II)acetylacetonate.<br />
The catalyst is easy to h<strong>and</strong>le, exhibits high activity for polymerization<br />
even in the presence of oxygen or an acidic compound, <strong>and</strong> imparts<br />
a suitable degree of surplus operation time. Catalysts that contain a metal<br />
compound for promoting the decomposition of the organic peroxide exhibit<br />
a particularly high polymerizing efficiency.<br />
If the polymerizable monomer is an acidic compound, e.g., 11-methacryloyloxy-1,1-undecanedicarboxylic<br />
acid (MAC-10), then there is no<br />
need to add any other acidic compound, <strong>and</strong> no acidic compound elutes<br />
out from the obtained cured product when it is used. The mechanism of<br />
initiation of polymerization is proposed as follows: The aryl borate compound<br />
is decomposed due to the acid compound. Thereby an aryl borane<br />
compound is formed which is then oxidized with oxygen present in the<br />
atmosphere to form polymerizable radicals. It is further oxidized with an<br />
organic peroxide to form more radicals in the composition containing less<br />
oxygen. Thereby it serves as a highly active catalyst for chemical polymerization.<br />
The metal compound promotes the decomposition of the organic<br />
peroxide. Oxidation of the aryl borane compound with the organic peroxide<br />
is promoted lending the catalyst itself for use as a more active catalyst<br />
for chemical polymerization. The polymerization proceeds at ambient<br />
temperature even in a dark place to give an excellently cured product. 24<br />
Several techniques have been reported for increasing the work-life,<br />
e.g., slowing the cure rate of the polymerizable system by reducing the<br />
amount of initiators, adding inhibitors, or adding comonomers to decelerate<br />
the cure rate of the free radical composition. 31 Examples for work-life<br />
extenders are allylsuccinic anhydride, 2-octen-1-ylsuccinic anhydride, iso-
672 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 19.5: Two Component Formulation 32<br />
Base paste %<br />
Pyrogenic silicic acid (particle size < 0.05 µ) 5.00<br />
Glass powder, silanized (average particle size 10 µ) 32.50<br />
2,2-Bis(4-(oligo(ethoxy))phenyl)propanedimethacrylate 61.48<br />
N,N-Dimethyl-p-toluidine 0.50<br />
Hydroquinone monomethyl ether 0.02<br />
Tributylborane 0.50<br />
Catalyst paste %<br />
Glass powder, silanized (average particle size 10 µ) 32.00<br />
2,2-Bis(4-(oligo(ethoxy))phenyl)propane diacetate 65.50<br />
Dibenzoyl peroxide 2.50<br />
butenylsuccinic anhydride, <strong>and</strong> itaconic anhydride.<br />
19.4.1.5 Hybrid Initiator Systems<br />
A hybrid initiator system acts on a mixture of epoxide monomers <strong>and</strong><br />
acrylic group-containing monomers. The epoxide monomers are cured by<br />
a cationic reaction mechanism. The acrylic group-containing monomers<br />
are cured by a radical mechanism.<br />
Two initiator systems are needed to ensure polymerization. 32 The<br />
first initiator system is comprised of boranes <strong>and</strong> hydrazones <strong>and</strong> releases<br />
species that initiate a curing reaction upon contact with oxygen. The second<br />
initiator system is comprised of iodonium compounds capable of radical<br />
fission.<br />
An oxygen-sensitive compound is used that, when brought into contact<br />
with oxygen, can form radicals that in turn can release acid from a<br />
saline initiator by means of another reaction sequence. The acid so formed<br />
can initiate a polymerization reaction, in particular a cationic polymerization<br />
reaction.<br />
This saline initiator is an iodonium compound, which, when activated<br />
by means of free radicals, can decompose into acids. Thus, there<br />
are two initiator systems which react with each other to control the course<br />
of the polymerization reaction. A two component material for temporary<br />
crowns <strong>and</strong> bridges, which is mixed in a ratio of 10/1 (base/catalyst) <strong>and</strong><br />
cured without any smear layer, is shown in Table 19.5. One special advantage<br />
of the preparations <strong>and</strong> processing techniques lies in the fact that the
Table 19.6: Photoinitiators for acrylics<br />
Compound<br />
Acrylic Dental Fillers 673<br />
Reference<br />
Benzil<br />
Camphorquinone<br />
8, 33<br />
Benzoin methyl ether<br />
Isopropoxybenzoin<br />
Benzoin phenyl ether<br />
Benzoin isobutyl ether<br />
Eosine<br />
33<br />
Titanocene<br />
33, 34<br />
range of the activation time <strong>and</strong> the processing time is determined by the<br />
composition of the dental materials. The processor can influence, within<br />
specific limits, the requisite processing time by means of the intensity with<br />
which the materials are brought into contact with oxygen or air.<br />
19.4.2 Photo Curing<br />
Light or photo curing or photosensitive polymerization initiation <strong>and</strong> curing<br />
systems are activated to harden <strong>and</strong> cure the composition by irradiation<br />
with visible or UV light. Visible light of a wavelength of about 400 to 500<br />
nm initiates rapid <strong>and</strong> efficient curing within a few minutes.<br />
Preferably, the photoinitiator systems should be sensitive to light in<br />
a range of wavelength that is not harmful to the patient who is undergoing<br />
a dental procedure. 25 Photoinitiators for acrylics are summarized in<br />
Table 19.6.<br />
Initiation by photo curing is achieved with α-diketone light-sensitive<br />
initiator compounds such as benzophenone or a derivative, or a 1,2-diketone<br />
such as benzil or camphorquinone (CQ) <strong>and</strong> derivatives. Certain<br />
tertiary aromatic amines act as accelerator compounds. Some compounds<br />
that may be suitable are ultraviolet light-sensitive initiators, like 1,2-diketones,<br />
benzophenones, substituted benzophenones, benzoin methyl ether,<br />
isopropoxybenzoin, benzoin phenyl ether, <strong>and</strong> benzoin isobutyl ether, as<br />
shown in Figure 19.6. An example for an effective photoinitiator system is<br />
camphorquinone (CQ) <strong>and</strong> ethyl-4-dimethylamino benzoate (EDMAB) or<br />
cyanoethylmethylaniline. 8<br />
The crosslinking density of the final product is dependent on the way<br />
the radiation energy is offered to the curing system. 35
674 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
H 3 C<br />
CH 3<br />
CH 3<br />
O<br />
O<br />
C<br />
O<br />
C<br />
O<br />
Camphorquinone<br />
Benzil<br />
H 3 C<br />
N<br />
H 3 C<br />
O<br />
C<br />
O CH 2 CH 3<br />
Ethyl 4-(dimethylamino)benzoate<br />
F<br />
N<br />
Ti<br />
F<br />
F<br />
F<br />
N<br />
Titanocene<br />
Figure 19.6: Photoinitiators
Acrylic Dental Fillers 675<br />
The photopolymerization or a Bis-GMA/TEGDMA resin was examined<br />
with light sources with extremely different intensities, i.e., 200 <strong>and</strong><br />
1800 mW/cm 2 ). In general, the polymers irradiated using the high light<br />
intensity source showed a greater conversion.<br />
However, an increased light intensity also increased the maximum<br />
temperature reached during polymerization. Therefore, the greater conversion<br />
results form both a photopolymerization <strong>and</strong> a thermal polymerization.<br />
Extreme differences in the initiation rate do not significantly alter the<br />
mechanical properties of the polymer matrix as long as the conversions are<br />
similar. 36<br />
The kinetics of the photopolymerization of dental composites has<br />
been monitored in-situ by a modified Fourier Transform infrared spectrometer<br />
with attenuated total reflection. The experimental setup could reveal<br />
the kinetic stages of the photopolymerization of dental composites. The<br />
spectroscopic results correlate with the Vickers micro-hardness. 37 Under<br />
comparable conditions, UDMA resins are significantly more reactive than<br />
Bis-GMA <strong>and</strong> EBADMA resins. 38<br />
In urethane dimethacrylate (UDMA) <strong>and</strong> triethylene glycol dimethacrylate<br />
(TEGDMA)-based dental resins, differential scanning calorimetry<br />
(DSC) showed that the light-cured specimens contain residual living<br />
groups entrapped by the fast reaction, which lead to further reaction during<br />
postcure heat treatment.<br />
After an additional heating to 175°C above the exothermic peak,<br />
most of the residual groups in the light-cured specimen were found to have<br />
reacted. A single decrease in modulus <strong>and</strong> a single peak in the tanδ curve,<br />
was observed <strong>and</strong> no exotherm in the DSC curve. 39<br />
19.4.2.1 Tertiary Amine Reductants<br />
In visible light curable compositions, the tertiary amines are most profitably<br />
acrylate derivatives such as dimethylaminoethyl methacrylate <strong>and</strong>,<br />
particularly, diethylaminoethyl methacrylate (DEAEMA) in amounts ranging<br />
from about 0.05 to about 0.5% of the resin composition. 9<br />
Other suitable tertiary amine reductants are tributylamine, tripropylamine,<br />
N-methyldiethanolamine, N-propyldiethanolamine, N-ethyldiisopropanolamine,<br />
triethanolamine <strong>and</strong> triisopropanolamine. One of the<br />
preferred tertiary amine reductants is ethyl-4-dimethylamino benzoate<br />
(EDMAB). 25
676 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
19.4.3 Curing Techniques<br />
Various techniques of curing are in use. Soft-start cure of a resin composite<br />
may give rise to a reduced contraction because of a possible flow before<br />
gelling. Soft-start cure may be achieved by a pulse-delay cure technique,<br />
where the polymerization is initiated by a short flash of light followed by<br />
a waiting time of several minutes before the final curing is performed.<br />
40, 41<br />
Another soft-start technique is characterized by step-curing. Here a reduced<br />
intensity of curing light is used during the first part of the polymerization<br />
period. Next the intensity is increased. 42 The use of a soft-start<br />
polymerization mode, from low to high, offers some modest advantages<br />
in curing effects, especially the delay in the original shrinkage-strain. In<br />
general, a higher conversion is accompanied by a higher shrinkage. Some<br />
reductions in the problems of shrinkage may be achieved by an acceptable<br />
reduction in degree of conversion.<br />
The pulse-cure method may give rise to a different structure of the<br />
polymer although the degree of conversion <strong>and</strong> the hardness in the final<br />
state are not affected by the curing method.<br />
43, 44<br />
An initially slow cure may favor the formation of a relatively linear<br />
polymer. A slow start of the polymerization could be associated with<br />
relatively few centers of polymer growth, resulting in a more linear polymer<br />
structure with relatively few crosslinks. The differences in structure<br />
can be examined by studies of the Wallace hardness of cured swollen samples.<br />
The Wallace hardness measures the depth of penetration of a Vickers<br />
diamond under a predetermined load. The Wallace hardness is in fact a<br />
measure of softness, in that the higher the Wallace hardness, the softer is<br />
the material. A lower degree of conversion is associated with softer polymers<br />
after storage in ethanol. <strong>Polymers</strong> with the same degree of conversion<br />
respond differently to the softening action by ethanol swelling, dependent<br />
on the history of light exposure. 45<br />
In a series of experiments using microwave curing of acrylic resins<br />
with different cure cycles, it was shown that the porosity of the cured resin<br />
was not affected by the manner of curing. 46<br />
19.4.4 Dual Initiator Systems<br />
Initiator systems employing two or more initiators, i.e., light <strong>and</strong> self-curing<br />
or light <strong>and</strong> heat initiated systems, can also be formulated.<br />
Such multi-initiator systems may have utility in that they may in-
Acrylic Dental Fillers 677<br />
clude a rapid cure initiator, <strong>and</strong> light or heat cure to impart significant polymerization<br />
in the dental office or dental laboratory. A light cure system in<br />
combination with a longer time self-cure initiator continues to cause further<br />
polymerization after the patient leaves the office <strong>and</strong> further secures<br />
the restorative to the tooth structure. 25<br />
Such dual cure light/heat systems, as well as their respective single<br />
initiator systems, are also desirable in that they may be formulated <strong>and</strong><br />
packaged in one container or syringe, thereby avoiding the need for mixing<br />
by the dental professional before application. For example, such one-component<br />
systems exhibit good shelf life of more than a year when stored<br />
away from light at room temperature.<br />
If self-curing compositions are desired, the self-curing initiator may<br />
be packaged in one of two containers separately from the polymerizable<br />
components of the composition, with the contents of both containers being<br />
admixed shortly before use in the dental office.<br />
19.5 INHIBITORS<br />
Polymerization inhibitors are mainly substituted phenols, for example,<br />
hydroquinone monomethyl ether (MEHQ) or 2,6-di-tert-butyl-4-methylphenol<br />
(BHT)<br />
19.6 ADDITIVES<br />
19.6.1 Fillers <strong>and</strong> Reinforcing Materials<br />
Fillers are summarized in Table 19.7. Filler particles can be silanized<br />
aluminum oxide, zirconium oxide, silicon oxide, barium glass, strontium<br />
glass, <strong>and</strong> silicate glasses. Spherical particles in the compositions improve<br />
the h<strong>and</strong>ling characteristics, such as bulk <strong>and</strong> consistency, <strong>and</strong> improve<br />
the filler packing for better restoration placement in cavity preparations by<br />
minimizing the flow <strong>and</strong> the slump of the composition. In most composites,<br />
fillers have a higher refractive index than the resin. Typical levels<br />
of filler are from about 50 to 80%. If a more finely particulated filler is<br />
used, the amounts of filler may be decreased due to the relative increase<br />
in surface area which attends the smaller sizes of particles. Particle size<br />
distributions may range from 0.02 to 50 µ.<br />
Both the chemical structure of the polymer matrix <strong>and</strong> the type of
678 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 19.7: Fillers for Dental Composites<br />
Material<br />
Reference<br />
Calcium hydroxy apatite<br />
Silanized aluminum oxide<br />
Zirconium oxide<br />
Siliconedioxide<br />
Barium glass<br />
Strontium glass<br />
Strontium fluoroaluminosilicate cement<br />
17<br />
Silicate glass<br />
Functionalized metal oxide nanoparticles<br />
Silsesquioxane<br />
9<br />
Polyamide 6 nanofibers<br />
47<br />
filler system can have significant effects on the strength <strong>and</strong> water sorption<br />
of dental composites. 48<br />
19.6.1.1 Sub-micron Size Fillers<br />
Sub-micron size fillers are preferred to minimize surface wear <strong>and</strong> plucking<br />
of filler components from the restorative surface, as well as imparting a<br />
surface which may be easily polished by the dental professional. Filler<br />
particles have an average size of about 0.04 to 0.08 µm. 25<br />
19.6.1.2 Glass Fibers<br />
Glass fibers increase filler packing <strong>and</strong> improve filler self-orientation for<br />
high filler loadings. 25<br />
19.6.1.3 Functionalized Metal Oxide Nanoparticles<br />
There have been efforts to generate functionalized metal oxide nanoparticles<br />
to make highly uniform composite materials. For example, aluminum<br />
tri-sec-butylate is dissolved in toluene, reacted with one allyl acetoacetate,<br />
49 c.f. Figure 19.7. The dispersed, individual metal oxide particles can<br />
be prepared by partially replacing the organic radical by a functional one<br />
<strong>and</strong> then by hydrolyzing to oxide with water.<br />
A silane functionalized polymer is also hydrolyzed with water to<br />
form a network crosslinked by the resultant silica particles. Elimination of
Acrylic Dental Fillers 679<br />
CH 3 CH 3<br />
CH CH 2<br />
O<br />
CH 2 CH O Al O CH CH 2<br />
CH 3 CH 3 CH 3 CH 3<br />
+<br />
CH 3<br />
O<br />
C CH 2 C<br />
O<br />
O CH 2 CH CH 2<br />
CH 3<br />
CH 3<br />
CH CH 2<br />
O<br />
CH 2 CH O Al O CH 2 CH CH 2<br />
CH 3 CH 3<br />
H 2 O<br />
O<br />
O<br />
Al O CH 2 CH CH 2<br />
O<br />
Al O CH 2 CH CH 2<br />
Figure 19.7: Functionalized Metal Oxide
680 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
the composite shrinkage induced by removal of volatile reaction products<br />
is attempted by utilizing ring strained alkenoxysilanes <strong>and</strong> polymerizable<br />
solvents where all reaction by-products contribute to the SiO 2 network or<br />
the resultant interpenetrating, matrix, organic polymer. The expected packing<br />
disruption induced by the strained ring opening of the alkenoxysilane<br />
is a strategy for compensating for the shrinkage induced by conversion of<br />
double bonds to single bonds. 16<br />
19.6.1.4 Polyamide 6 Nanofiber<br />
Electrospun Polyamide 6 nanofibers, as non-woven fabrics, were impregnated<br />
with the dental methacrylate of 2,2-bis[4-(3-methacryloxy-2-hydroxypropoxy)phenyl]propane/triethylene<br />
glycol dimethacrylate (Bis-G-<br />
MA/TEGDMA) in order to prepare restorative composite resins. 47<br />
The polyamide 6 nanofibers used are much softer than inorganic<br />
fillers with a regular cylindrical shape with diameters ranging from 100<br />
to 600 nm. Flexural strength (FS), elastic modulus (EY), <strong>and</strong> work of<br />
fracture (WOF) of the nanofiber reinforced composite resins were significantly<br />
increased by the admixture of relatively small amounts of Polyamide<br />
6 nanofibers.<br />
19.6.1.5 Silsesquioxane<br />
A polyhedral oligomeric silsesquioxane (POSS) filler has several advantages.<br />
POSS-filled resins typically exhibit lower mass densities <strong>and</strong> greater<br />
stiffness, <strong>and</strong> are capable of withst<strong>and</strong>ing higher temperatures, as well as<br />
higher levels of ionizing radiation. In addition, POSS-filled resins are capable<br />
of wetting fibers to desirably high degrees. The use of POSS with<br />
dental resin materials, particularly the acrylate or methacrylate resins, minimizes<br />
polymerization shrinkage <strong>and</strong> increases material toughness. The<br />
nanoscale dimensionality of the POSS fillers also allows for better aesthetic<br />
properties, including easier polishability <strong>and</strong> improved transparency. 9<br />
Functionalized POSS, also known as POSS monomers are particularly<br />
preferred. Herein one or more of the covalently bound organic groups<br />
are reactive with at least one component of the resin composition. In some<br />
cases, it is possible to have all of the covalently bound organic groups be<br />
reactive. POSS monomers may be prepared, for example, by corner-capping<br />
an incompletely condensed POSS, containing trisilanol groups with a<br />
substituted trichlorosilane.
Acrylic Dental Fillers 681<br />
Through variation of the substituted group on the silane, a variety<br />
of functional groups can be placed off the corner of the POSS framework,<br />
including halide, alcohol, amine, isocyanate, acid, acid chloride, silanols,<br />
silane, acrylate, methacrylate, olefin, <strong>and</strong> epoxide. Preferred functional<br />
groups are acrylate <strong>and</strong> methacrylate groups since they are involved in the<br />
polymerization reaction.<br />
19.6.1.6 Calcium Phosphates<br />
Amorphous calcium phosphates (ACP) are fillers for mineral releasing<br />
dental composites. When the ACP is stabilized by pyrophosphate (P 2 O 4−<br />
7 )<br />
ions, pyrophosphate retards the conversion of ACP to apatite. ACPs have<br />
a relatively high aqueous solubility <strong>and</strong> can release Ca 2+ <strong>and</strong> PO 4− ions.<br />
However, pyrophosphate stabilized ACP-filled composites have relatively<br />
poor mechanical properties, because ACP does not act as reinforcing filler<br />
such as commonly used silanized glass fillers.<br />
ACP can be hybridized with tetraethoxysilane or zirconyl chloride<br />
(ZrOCl 2 ) <strong>and</strong> surface-treated with 3-methacryloxypropoxytrimethoxysilane<br />
(MPTMS) or zirconyl dimethacrylate (ZrDMA). In fact, a silica- or zirconia-hybridized<br />
ACP moderately improves the biaxial flexural strength of<br />
Bis-GMA/TEGDMA/HEMA/ZrDMA-based composites while maintaining<br />
their high anti-demineralizing <strong>and</strong> remineralizing potential. Thus adequate<br />
levels of calcium <strong>and</strong> phosphate ions are released. 50<br />
19.6.2 Pigments<br />
For aesthetic dem<strong>and</strong>s, pigments are added to provide the desired colors of<br />
the fillings, i.e., the colors of the neighboring teeth. Pigments are inorganic<br />
compounds of different kinds <strong>and</strong> blendings.<br />
There have been attempts to st<strong>and</strong>ardize color shades to facilitate<br />
clinical use <strong>and</strong> combining products. Many producers have adapted their<br />
color system to the Vita R shade system (Vita Zahnfabrik Company, Germany)<br />
<strong>and</strong> deliver a full range of shades in one-dose pre-filled tips.<br />
19.6.3 Photostabilizers<br />
In order to protect the materials against photo degradation, photostabilizers<br />
are added. Photo degradation of the cured resin causes changes in color <strong>and</strong><br />
the mechanical properties. Most common photostabilizers are salicylates,
682 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
in particular the phenyl esters of benzoic acid, ortho-hydroxybenzophenones,<br />
ortho-hydroxybenzotriazoles <strong>and</strong> substituted cinnamic esters. A few<br />
photostabilizers are shown in Figure 19.8.<br />
19.6.4 Caries Inhibiting Agents<br />
Caries is the damage of bone tissue (not only dental) caused by infection.<br />
Caries dentium is the tooth decay where the dental enamel, i.e., dentin is<br />
damaged by bacteria residing in the mouth.<br />
Increased dental plaque supports the formation of acid metabolic<br />
products of the bacteria that act in the decalcination of the dentin. Moreover,<br />
sucrose acts in a similar way, as it forms dextranes that stick as<br />
plaques <strong>and</strong> decompose into lactic acid <strong>and</strong> pyruvic acid.<br />
Caries inhibiting agents are slow releasing fluoride agents to help<br />
inhibit caries from forming in the adjacent tooth structure.<br />
19.6.5 Coloring or Tint Agents<br />
Coloring or tint agents may be included in small amounts of about 1%<br />
or less of the total composition. Such fillers can also be selected to be<br />
radio opaque. For example, appropriate amounts of radio opaque barium,<br />
strontium, or zirconium glass may be used as all or as part of the filler<br />
portion.<br />
19.6.6 Adhesion Promoter<br />
The compositions may include an adhesion promoter. This may be a<br />
phosphorus-containing adhesion promoter, free from halogen atoms. Both<br />
polymerizable <strong>and</strong> non-polymerizable phosphorus derivatives are available.<br />
However polymerizable phosphorus materials having ethylenic unsaturation<br />
are advantageous.<br />
Examples of saturated <strong>and</strong> unsaturated phosphorus acid esters are<br />
shown in Table 19.8. The phosphoric ester of Bis-GMA can be obtained<br />
by the treatment of Bis-GMA with phosphorous oxychloride, as shown in<br />
Figure 19.10.
Acrylic Dental Fillers 683<br />
O<br />
OH<br />
O<br />
OH<br />
OH<br />
OC 8 H 17<br />
2,4-Dihydroxybenzophenone<br />
2-Hydroxy-4-octoxybenzophenone<br />
NC<br />
O<br />
O<br />
NC<br />
O<br />
O<br />
C<br />
O<br />
O<br />
CN<br />
O<br />
O<br />
CN<br />
1,3-bis-[2’-cyano-3’,3-diphenylacryloyl)oxy]-2,2-bis-<br />
{[2-cyano-3’,3’-diphenylacryloyl)oxy]methyl}propane<br />
Figure 19.8: 2,4-Dihydroxybenzophenone (Uvinul 3000 , BASF) 2-Hydroxy-4-octoxybenzophenone<br />
(Uvinul 3008 ) 1,3-Bis[2 ′ -cyano-3 ′ ,3-diphenylacryloyloxy]-2,2-bis-[[2-cyano-3<br />
′ ,3 ′ -diphenylacryloyloxy]methyl]propane (Uvinul<br />
3030)
684 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Compound<br />
Table 19.8: Adhesion Promoters<br />
Reference<br />
Pentaerythritol triacrylate monophosphate<br />
17<br />
Pentaerythritol trimethacrylate monophosphate<br />
17<br />
Dipentaerythritol pentaacrylate monophosphate<br />
17<br />
Dipentaerythritol pentamethacrylate monophosphate<br />
17<br />
Hydroxyethyl methacrylate monophosphate<br />
17<br />
Methacryloyloxyethane-1,1-diphosphonic acid<br />
51<br />
Methacrylate-terminated phosphoric acid ester<br />
7<br />
4-Methacryloxyethyl trimellitate<br />
52<br />
2,2 ′ -Bis(α-methacryloxy-β-hydroxypropoxyphenyl)propane<br />
diphosphonate<br />
Bis-GMA diphosphonate<br />
Bis-GMA diphosphate<br />
Dibutyl phosphite<br />
Di-2-ethylhexyl phosphite<br />
Di-2-ethylhexyl phosphate<br />
Glyceryl-2-phosphate<br />
Glycerophosphate dimethacrylate<br />
53<br />
Glycerophosphoric acid<br />
Methacryloxyethyl phosphate<br />
Glyceryl dimethacrylate phosphate<br />
CH 3<br />
H 2 C<br />
H 2 C C C O<br />
O<br />
CH 3 O CH 2<br />
C C O CH 2 C CH 2 O<br />
CH 3 CH 2<br />
H 2 C C O<br />
O<br />
OH<br />
P<br />
OH<br />
O<br />
Figure 19.9: Pentaerythritol trimethacrylate monophosphate
Acrylic Dental Fillers 685<br />
C<br />
CH 2<br />
CH 3<br />
C<br />
CH 2<br />
CH 3<br />
C<br />
O<br />
C<br />
O<br />
O<br />
O<br />
CH 2<br />
CH 2<br />
OH<br />
CH<br />
OH<br />
CH<br />
O<br />
P<br />
O<br />
CH 2<br />
CH 2<br />
OH<br />
O<br />
Cl<br />
O<br />
Cl<br />
P<br />
O , H 2 O<br />
Cl<br />
H 3 C<br />
C CH 3<br />
H 3 C<br />
C CH 3<br />
O<br />
O<br />
CH 2<br />
CH 2<br />
OH<br />
CH<br />
OH<br />
CH<br />
O<br />
P<br />
O<br />
CH 2<br />
CH 2<br />
OH<br />
O<br />
O<br />
C<br />
O<br />
C<br />
O<br />
C<br />
CH 3<br />
C<br />
CH 3<br />
CH 2<br />
CH 2<br />
Figure 19.10: Phosphoric ester of Bis-GMA 51
686 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
19.6.7 Thermochromic Dye<br />
For aesthetic reasons, tooth-colored restoration materials are increasingly<br />
being used in restorative dentistry. These materials have the disadvantage<br />
that they can be visually distinguished from the natural tooth substance<br />
only with difficulty, with the result that the removal of excess material <strong>and</strong><br />
also the reworking <strong>and</strong> matching of fillings is made difficult. The consequence<br />
is that, frequently, healthy tooth substance is unnecessarily removed<br />
or on the other h<strong>and</strong>, excess dental material is overlooked which can<br />
then, as a retention niche, encourage the formation of plaque <strong>and</strong> lead to<br />
periodontal problems. Also, when tooth-colored fillings are removed, because<br />
of the poor visibility of the transition area between filling <strong>and</strong> tooth<br />
substance, often either too much healthy tooth substance is removed or remains<br />
of the filling are overlooked. Similar problems result when using<br />
tooth-colored fixing materials for the cementing of tooth-colored restorations.<br />
A dental material can be formulated, where the color can be temporarily<br />
changed in a simple way such that the material can be visually<br />
distinguished from the natural tooth substance, but assumes its original<br />
color after a period sufficient for the working of the dental material. This<br />
object is achieved by adding a thermochromic dye to the formulation.<br />
Thermochromic dyes are preferred that are colorless at a temperature<br />
of approx. 37°C <strong>and</strong> which change color upon heating or preferably<br />
cooling, i.e., assume a color that can clearly be distinguished from the natural<br />
tooth substance. At a temperature of 37°C, the color of the dental<br />
material is thus determined by its intrinsic color.<br />
Thermochromic dyes are based on an acid-responsive component<br />
<strong>and</strong> an acidic component. Other thermochromic dyes are liquid crystalline<br />
cholesterol derivatives. 54<br />
19.7 PROPERTIES<br />
Dental materials are st<strong>and</strong>ardized by several documents.<br />
55, 56<br />
19.7.1 Water Sorption<br />
According to the ISO st<strong>and</strong>ard for dental restorative resins, a suitable resin<br />
for its use as dental material must show a water sorption lower than
Acrylic Dental Fillers 687<br />
50 µg/mm 3 <strong>and</strong> a solubility lower than 5 µg/mm 3 . 57 In resins <strong>and</strong> composites<br />
based on an ethoxylated bisphenol A glycol dimethacrylate (Bis-<br />
EMA) <strong>and</strong> a poly(carbonate)dimethacrylate (PCDMA), the water sorption<br />
<strong>and</strong> desorption was examined in both equilibrium <strong>and</strong> dynamic conditions<br />
in adjacent sorption-desorption cycles. The equilibrium water uptake from<br />
all resins was very small. However, it increased as the amount of PCDMA<br />
in the resin was increased. 58 A maximum volume increase of 2% due to<br />
swelling was observed.<br />
The sorption of water of polymer filling materials affects the dimensional<br />
stability, the mechanical properties, <strong>and</strong> the bonding strength to the<br />
tooth. The maximum water sorption <strong>and</strong> the diffusion coefficient of water<br />
are important in determining the time-dependent mechanical properties<br />
<strong>and</strong> time-dependent hydroscopic expansion of resins for clinical use. 59<br />
19.7.2 Cytotoxicity<br />
Acrylic resins have been shown to be cytotoxic as a result of the substances<br />
that leach from the resin. The primary eluate is residual monomer. 60 However,<br />
in organic leachables analyzed by gas chromatography-mass spectrometry,<br />
nearly the whole volatile compounds in the formulation as well<br />
as degradation products could be traced back. Among components detected<br />
were monomers, comonomers, initiators, stabilizers, decomposition<br />
products, <strong>and</strong> contaminants. In a study, 32 substances were identified <strong>and</strong><br />
17 were confirmed with reference substances. 61 In order to minimize the<br />
cytotoxicity, utmost conversion must be achieved <strong>and</strong> monomers with minimal<br />
cytotoxicity should be selected. Common compounds in dental resin<br />
compositions have been tested with respect to estrogenic activity. Most<br />
compounds tested in the study do not show estrogenic activity, but some<br />
show activity. 62<br />
19.8 APPLICATIONS<br />
19.8.1 Filling Techniques<br />
Compositions are applied to the tooth, preferably by syringe in incremental<br />
layers of about 0.5 to about 2 mm <strong>and</strong> cured for about 20 to 40 seconds, depending<br />
on the shade of the composition. Darker compositions have longer<br />
curing times. Additional layers follow until the cavity is completely filled<br />
to the cavosurface margin. Any excess material is removed immediately
688 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
from the surface <strong>and</strong> the restoration is finished <strong>and</strong> polished by conventional<br />
techniques such as diamonds, discs <strong>and</strong> polishing pastes. Such finishing<br />
also removes any oxygen-inhibited uncured or partially cured layer<br />
on the surface of the restoration, which if left in place, might cause staining<br />
of the surface over time. 25<br />
19.8.2 Primer Emulsions<br />
A self-etching dental adhesive primer composition is used as an adhesive or<br />
adhesion promoter to affix dental filling materials or bone cements to tooth<br />
material. Such a composition essentially comprises an emulsion of water<br />
immiscible polymerizable monomers, oligomers, <strong>and</strong> adhesion promoters<br />
in water. By using an emulsion of the polymerizable substances in water,<br />
the need for volatile organic solvents is avoided <strong>and</strong> biocompatibility is<br />
enhanced.<br />
Further, the composition comprises initiators, accelerators, <strong>and</strong> inhibitors<br />
<strong>and</strong> surfactants <strong>and</strong> colloidal silica particles to aid in the formulation<br />
of an emulsion <strong>and</strong> to help keep this stable.<br />
For example, a polymerizable surfactant may consist of the reaction<br />
product of isophorone diisocyanate with poly(ethylene glycol) monomethyl<br />
ether, cured with dibutyltin dilaurate. To this product glycerol<br />
dimethacrylate is added together with a radical polymerization inhibitor,<br />
which grafts to the polyurethane polymer. 63 The product is a white, soft<br />
sticky solid at room temperature, partially soluble in water to give a light<br />
foam on shaking. The material has a melting range of about 35 to 37°C.<br />
The polymeric <strong>and</strong> polymerizable surfactant can be emulsified in water <strong>and</strong><br />
phosphoric acid which provides the etching.<br />
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evolution of the mechanical properties of dental composites. Polymer Testing,<br />
22(1):77–81, February 2003.<br />
38. S. H. Dickens, J. W. Stansbury, K. M. Choi, <strong>and</strong> C. J. E. Floyd. Photopolymerization<br />
kinetics of methacrylate dental resins. Macromolecules, 36(16):<br />
6043–6053, August 2003.<br />
39. J. K. Lee, J. Y. Kim, <strong>and</strong> B. S. Lim. Dynamic mechanical properties of a<br />
visible light curable urethane dimethacrylate based dental resin. Polym. J.,<br />
35(11):890–895, 2003.<br />
40. J. Kanca, III. <strong>and</strong> B. I. Suh. Pulse activation: reducing resin-based composite<br />
contraction stresses at the enamel cavosurface margins. American Journal of<br />
Dentistry, 12(3):107–112, June 1999.<br />
41. A. Sahafi, A. Peutzfeldt, <strong>and</strong> E. Asmussen. Effect of pulse-delay curing on<br />
in vitro wall-to-wall contraction of composite in dentin cavity preparations.<br />
American Journal of Dentistry, 14(5):295–296, October 2001.<br />
42. N. Silikas, G. Eliades, <strong>and</strong> D. C. Watts. Light intensity effects on resincomposite<br />
degree of conversion <strong>and</strong> shrinkage strain. Dent. Mater., 16(4):<br />
292–296, July 2000.<br />
43. E. Asmussen <strong>and</strong> A. Peutzfeldt. Influence of pulse-delay curing on softening<br />
of polymer structures. Journal of Dental Research, 80(6):1570–1573, June<br />
2001.<br />
44. E. Asmussen <strong>and</strong> A. Peutzfeldt. Influence of selected components on crosslink<br />
density in polymer structures. Eur. J. Oral Sci., 109(4):282–285, August<br />
2001.<br />
45. E. Asmussen <strong>and</strong> A. Peutzfeldt. Two-step curing: influence on conversion<br />
<strong>and</strong> softening of a dental polymer. Dent. Mater., 19(6):466–470, September<br />
2003.<br />
46. M. A. Compagnoni, D. B. Barbosa, R. F. de Souza, <strong>and</strong> A. C. Pero. The<br />
effect of polymerization cycles on porosity of microwave-processed denture<br />
base resin. J. Prosthet. Dent., 91(3):281–285, March 2004.<br />
47. H. Fong. Electrospun nylon 6 nanofiber reinforced Bis-GMA/TEGDMA dental<br />
restorative composite resins. Polymer, 45(7):2427–2432, March 2004.<br />
48. D. Skrtic <strong>and</strong> J. M. Antonucci. Effect of bifunctional comonomers on mechanical<br />
strength <strong>and</strong> water sorption of amorphous calcium phosphate- <strong>and</strong><br />
silanized glass-filled Bis-GMA-based composites. Biomaterials, 24(17):<br />
2881–2888, August 2003.
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49. R. Nass <strong>and</strong> H. Schmidt. Process for fixing inorganic species in an organic<br />
matrix. US Patent 5 064 877, assigned to Fraunhofer-Gesellschaft zur<br />
Forderung der Angew<strong>and</strong>ten Forschung e.V. (DE), November 12 1991.<br />
50. D. Skrtic, J. M. Antonucci, E. D. Eanes, <strong>and</strong> N. Eidelman. Dental composites<br />
based on hybrid <strong>and</strong> surface-modified amorphous calcium phosphates.<br />
Biomaterials, 25(7-8):1141–1150, March–April 2004.<br />
51. I. Omura, J. Yamauchi, Y. Nagase, <strong>and</strong> F. Uemura. Adhesive compositions.<br />
US Patent 4 499 251, assigned to Kuraray Co., Ltd. (Kurashiki, JP), February<br />
12 1985.<br />
52. E. Masuhara, N. Nakabayashi, <strong>and</strong> M. Takeyama. Curable composition. US<br />
Patent 4 148 988, assigned to Mitsui Petrochemical Industries Ltd. (Tokyo,<br />
JP), April 10 1979.<br />
53. L. J. Pranitis, Jr. <strong>and</strong> D. Ng. Single dose dental adhesive delivery system <strong>and</strong><br />
method <strong>and</strong> adhesive therefor. US Patent 5 860 806, assigned to The Kerr<br />
Corporation (Orange, CA), January 19 1999.<br />
54. A. Burgath, P. Burtscher, U. Salz, <strong>and</strong> V. Rheinberger. Thermochromic dental<br />
material. US Patent 6 670 436, assigned to Ivoclar Vivadent AG (LI),<br />
December 30 2003.<br />
55. Dentistry – polymer-based filling, restorative <strong>and</strong> luting materials. ISO St<strong>and</strong>ard<br />
4049, International Organization for St<strong>and</strong>ardization, Geneva, Switzerl<strong>and</strong>,<br />
2000.<br />
56. Dentistry – polymer-based die materials. ISO St<strong>and</strong>ard 14233, International<br />
Organization for St<strong>and</strong>ardization, Geneva, Switzerl<strong>and</strong>, 2003.<br />
57. I. Sideridou, V. Tserki, <strong>and</strong> G. Papanastasiou. Study of water sorption, solubility<br />
<strong>and</strong> modulus of elasticity of light-cured dimethacrylate-based dental<br />
resins. Biomaterials, 24(4):655–665, February 2003.<br />
58. I. Sideridou, D. S. Achilias, C. Spyroudi, <strong>and</strong> M. Karabela. Water sorption<br />
characteristics of light-cured dental resins <strong>and</strong> composites based on bis-E-<br />
MA/PCDMA. Biomaterials, 25(2):367–376, January 2004.<br />
59. K. Asaoka <strong>and</strong> S. Hirano. Diffusion coefficient of water through dental composite<br />
resin. Biomaterials, 24(6):975–979, March 2003.<br />
60. J. H. Jorge, E. T. Giampaolo, A. L. Machado, <strong>and</strong> C. E. Vergani. Cytotoxicity<br />
of denture base acrylic resins: A literature review. J. Prosthet. Dent., 90(2):<br />
190–193, August 2003.<br />
61. V. B. Michelsen, H. Lygre, R. Skalevik, A. B. Tveit, <strong>and</strong> E. Solheim. Identification<br />
of organic eluates from four polymer-based dental filling materials.<br />
Eur. J. Oral Sci., 111(3):263–271, June 2003.<br />
62. Y. Nomura, H. Ishibashi, M. Miyahara, R. Shinohara, F. Shiraishi, <strong>and</strong><br />
K. Arizono. Effects of dental resin metabolites on estrogenic activity in vitro.<br />
J. Mater. Sci. -Mater. Med., 14(4):307–310, April 2003.<br />
63. G. B. Blackwell. Self etching adhesive primer composition <strong>and</strong> polymerizable<br />
surfactants. US Patent 6 387 982, assigned to Dentsply DeTrey G.m.b.H.<br />
(DE), May 14 2002.
20<br />
Toners<br />
Toners for developing electrical or magnetic latent images are used in various<br />
processes for forming <strong>and</strong> printing images. One such image forming<br />
process is electrophotography, which uses a photosensitive member generally<br />
formed of a photo conductive material, <strong>and</strong> wherein an electrical latent<br />
image is formed on the photosensitive member by various means. The<br />
electrical latent image is developed using a toner. The toner image thus developed<br />
is transferred to a printing material, such as paper, <strong>and</strong> then fixed<br />
thereto by heating or pressure, or by using solvent vapor thus obtaining a<br />
copy of the image. 1 The following types of developers are conventionally<br />
used in dry development devices for electrophotography:<br />
1. One-component-type magnetic developers comprising a toner containing<br />
magnetic powder.<br />
2. One-component-type non magnetic developers comprising a toner<br />
containing no magnetic powder.<br />
3. Two-component-type non magnetic developers comprising a toner<br />
containing no magnetic powder <strong>and</strong> a magnetic carrier, which is<br />
mixed with the toner in a fixed proportion.<br />
4. Two-component-type magnetic developers comprising a toner containing<br />
magnetic powder <strong>and</strong> a magnetic carrier, which is mixed<br />
with the toner in a fixed proportion.<br />
Various development methods using such toners have been proposed<br />
<strong>and</strong> put into practical use. The toners used in these development methods<br />
693
694 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
are generally manufactured by a pulverizing method in which a coloring<br />
agent, like a dye or pigment, is mixed with, <strong>and</strong> uniformly dispersed in,<br />
a thermoplastic resin serving as the binder. The mixed substance thus obtained<br />
is then finely pulverized <strong>and</strong> classified to provide a desired particle<br />
size distribution. Toners typically contain a principal resin or toner resin,<br />
colorant, <strong>and</strong> various functional additives such as release agents <strong>and</strong> charge<br />
control additives.<br />
Most toner compositions employ release agents such as waxes <strong>and</strong>/or<br />
silicone polymers. Poly(dimethylsiloxane) resins or oils exhibit excellent<br />
external release agent characteristics, i.e., when applied to fuser rolls, due<br />
to their extremely low surface energy. The property is highly desirable<br />
in contact-fusing electrophotography, because it is important to be able to<br />
release the toner from the hot-oiled fuser roll <strong>and</strong> thus prevent hot offset.<br />
Several different low molecular weight organic materials have been used<br />
in the toner industry to eliminate this hot offset phenomenon. Low molecular<br />
weight polyolefin waxes are by far the most common type of internal<br />
release agent.<br />
Each type of release agent has its own advantages <strong>and</strong> disadvantages.<br />
For example, polyolefins tend to crystallize to a significant extent.<br />
The crystallinity is between 70% <strong>and</strong> 90%. When these molecules crystallize,<br />
they segregate from the toner resin into a separate phase <strong>and</strong> form<br />
large wax domains which cause numerous print quality defects, as well as a<br />
wax imbalance between the toner fines <strong>and</strong> the average size toner particles.<br />
Poor homogeneity of these additives in the toner particles tends to cause a<br />
number of problems. The most important issues are low toner powder flow<br />
<strong>and</strong> variations in triboelectric charge distribution, which can lead to print<br />
quality defects.<br />
20.1 TONER COMPONENTS<br />
Toners contain a primary or binder resin, known as a toner resin, such as<br />
a thermoplastic resin, a colorant such as a dye or pigment, <strong>and</strong> a charge<br />
control agent, releasing agents, <strong>and</strong> other additives.<br />
Several polymers are usable as the thermoplastic binder resin, including<br />
poly(styrene)s, styrene-acrylic resins, styrene-methacrylic resins,<br />
polyesters, epoxy resins, acrylics, <strong>and</strong> urethanes. 2, 3<br />
Examples of the colorant include: dyes <strong>and</strong> pigments such as<br />
carbon black, iron black, graphite, nigrosine, metallic complex of mono-
Toners 695<br />
azo dye, ultramarine, copper phthalocyanine, methylene blue, chrome yellow,<br />
quinoline yellow, hanza yellow, benzene yellow, <strong>and</strong> various types of<br />
quinacridone pigments. When the colorant is contained in a non magnetic<br />
toner, the amount should be approximately 1% to 30%, in magnetic toners,<br />
ca. 60%. The colorant can be coated by a UV stabilizer. 4<br />
Toner compositions can contain charge enhancing additives, for example,<br />
0.1% to 10% cetyl pyridinium chloride, distearyl dimethyl ammonium<br />
methyl sulfate, metal salicylates, etc. Other charge control agents include<br />
the sulfonated styrene-acrylate ester copolymers, calixarenes. Polymeric<br />
charge control agents can be compatibilized with the toner resin in<br />
the same manner as other polymeric components of the toner compositions.<br />
Toner compositions may also include colloidal silica, metal salts <strong>and</strong><br />
metal salts of fatty acids such as zinc stearate as surface additives.<br />
20.2 TONER RESINS<br />
The heterogeneity of the toner particles in the composition is believed to<br />
be the root cause of numerous problems throughout the serviceable life of<br />
toner in a printing device. The print quality black-on-white defect involving<br />
unwanted toner black spots on the printed product has been a recurring<br />
<strong>and</strong> sometimes serious problem in certain commercial printers. The black<br />
spots are highly visible in the background region of the print <strong>and</strong> are nonrepeating<br />
in nature.<br />
It is believed that the toner particle compositional uniformity is a<br />
major factor in the existence of such defects. Heterogeneity of the toner<br />
particles’composition is believed to be the root cause of observed selectivity<br />
throughout the life of the cartridge.<br />
The lack of heterogeneity in toners can be eliminated by the addition<br />
of two functional additives reactive with each other to form a stable reaction<br />
product. The copolymer reaction product apparently acts as a compatibilizer<br />
to improve the dispersion of various polymeric components, such<br />
as a release agent with the backbone structure of the toner resin.<br />
Toners contain a primary or binder resin, known as a toner resin,<br />
such as a thermoplastic resin, a colorant such as a dye or pigment, a charge<br />
control agent, releasing agents, <strong>and</strong> other additives. These components will<br />
be separately described.<br />
Any suitable binder resin can be used as the toner resin, including<br />
polyesters, epoxy resins, various polymers containing styrene, <strong>and</strong> acrylic
696 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Table 20.1: Toner Composition 1<br />
Component %<br />
Resin binder 90.0<br />
Carbon black 5.0<br />
Metal salicylate 2.5<br />
Poly(ethylene) wax 1.0<br />
Other additives 1.0<br />
Siloxane polymer 0.25<br />
Styrene-maleic anhydride copolymer 0.5<br />
Amino-siloxane polymer 0.25<br />
acid derivatives. These may be used either singly or as mixtures.<br />
Polyesters are not preferred, because it is difficult to place reactive<br />
functional groups on a polyester resin backbone <strong>and</strong> because polyester resins<br />
are more reactive than styrene polymers, increasing the tendency to<br />
obtain r<strong>and</strong>om copolymers rather than block or graft copolymers.<br />
The polymer used for toner preparations can be a r<strong>and</strong>om styrene/-<br />
acrylic copolymer, crosslinked with divinylbenzene. The two functional<br />
materials added to the toner formulation, which already contains a poly(dialkylsiloxane)<br />
oil, are a styrene/maleic anhydride copolymer <strong>and</strong> a diamine-terminated<br />
poly(dimethylsiloxane) polymer. The reaction takes place<br />
between the amino end groups <strong>and</strong> the anhydride side groups. During the<br />
extrusion <strong>and</strong> melt mixing of the toner materials, these functional groups<br />
react to form a fairly stable amic acid bond <strong>and</strong> thus, a polysiloxane/toner<br />
resin compatibilizer. An example for a toner composition with a styrenemaleic<br />
anhydride copolymer <strong>and</strong> an amino-siloxane polymer as compatibilizing<br />
agents is shown in Table 20.1.<br />
<strong>Reactive</strong> extrusion is accomplished in a continuous twin-screw extruder<br />
maintained within a temperature range of 135 to 210°C <strong>and</strong> at an appropriate<br />
torque. The molten extrudate is subsequently cooled by passage<br />
through a chilled roller assembly <strong>and</strong> the resulting ribbons are crushed. 1<br />
20.3 MANUFACTURE OF TONER RESINS<br />
20.3.1 Suspension Polymerization<br />
A suspension polymerization method for the preparation of a toner has<br />
been described. 5, 6 The organic phase, containing styrene monomer, n-
Toners 697<br />
butyl acrylate, divinylbenzene, 2,2 ′ -azobis(isobutyronitrile), paraffin <strong>and</strong><br />
Phthalocyanine Blue T, is dispersed into the aqueous phase. The aqueous<br />
phase contains polyvinyl alcohol <strong>and</strong> sodium dodecylsulfate as suspension<br />
dispersants. Infrared studies suggest that the interactions between Phthalocyanine<br />
Blue T <strong>and</strong> the resin are mainly caused by physical forces.<br />
20.3.2 Terephthalic Ester Resins<br />
The toner particles are prepared by an emulsion aggregation process. 7 The<br />
toner resin is a sulfonated polyester made from dimethyl terephthalate, sodium<br />
sulfoisophthalate, 1,2-propanediol, <strong>and</strong> 2.5 mol-% diethylene glycol<br />
with dibutyltin oxide as catalyst. Subsequent to synthesis of the toner particles<br />
<strong>and</strong> addition of pigment, poly(pyrrole) is applied to the toner particle<br />
surfaces by an oxidative polymerization process. Using oxidants such as<br />
ferric chloride <strong>and</strong> tris(p-toluenesulfonato)iron(III) for the oxidative polymerization<br />
of the pyrrole monomer tends to result in formation of toner<br />
particles that become positively charged when subjected to triboelectric or<br />
inductive charging processes. Accordingly, toner particles can be obtained<br />
with the desired charge polarity without the need to change the toner resin<br />
composition, <strong>and</strong> can be achieved independently of any dopant used with<br />
the poly(pyrrole). The poly(pyrrole) in or on the toner particles generally<br />
imparts a high degree of color to the toner particle. These toners are usually<br />
preferred, where black images are desired. Similarly to pyrrole monomers,<br />
3,4-ethylenedioxythiophene can be polymerized on the toner resin. 8<br />
20.3.3 Unsaturated Ester Resins<br />
Examples of linear unsaturated polyesters are low molecular weight condensation<br />
polymers formed by saturated <strong>and</strong> unsaturated diacids <strong>and</strong> diols.<br />
The resulting unsaturated polyesters are crosslinkable in two ways:<br />
1. Due to double bonds along the polyester chain, <strong>and</strong><br />
2. Due to the functional groups such as carboxyl, hydroxy, <strong>and</strong> others,<br />
amenable to acid-base reactions.<br />
Suitable diacids <strong>and</strong> dianhydrides include succinic acid, isophthalic<br />
acid, terephthalic acid, phthalic anhydride, <strong>and</strong> tetrahydrophthalic anhydride.<br />
Unsaturated diacids or anhydrides, are fumaric acid, itaconic acid,<br />
<strong>and</strong> maleic anhydride. Suitable diols include propylene glycol, ethylene<br />
glycol, diethylene glycol, <strong>and</strong> propoxylated bisphenol A.
698 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
A particularly preferred polyester is poly(propoxylated bisphenol A<br />
fumarate). A propoxylated bisphenol A fumarate unsaturated polymer undergoes<br />
a crosslinking reaction with a chemical crosslinking initiator, such<br />
as 1,1-di-(tert-butylperoxy)cyclohexane. The crosslinking between chains<br />
will produce a large, high molecular weight molecule, ultimately forming<br />
a gel.<br />
The toners <strong>and</strong> toner resins may be prepared by a reactive melt mixing<br />
process wherein reactive resins are partially crosslinked. For example,<br />
low melt toner resins <strong>and</strong> toners may be fabricated by a reactive melt mixing<br />
process comprising the following steps. 4<br />
1. Melting reactive base resin, thereby forming a polymer melt, in a<br />
melt mixing device.<br />
2. Initiating crosslinking of the polymer melt with certain liquid<br />
chemical crosslinking initiator <strong>and</strong> increased reaction temperature.<br />
3. Retaining the polymer melt in the melt mixing device for a sufficient<br />
residence time that partial crosslinking of the base resin may<br />
be achieved.<br />
4. Providing sufficiently high shear during the crosslinking reaction<br />
to keep the gel particles formed during crosslinking small in size<br />
<strong>and</strong> well distributed in the polymer melt.<br />
5. Optionally devolatilizing the polymer melt to remove any effluent<br />
volatiles.<br />
The high temperature reactive melt mixing process allows for very<br />
fast crosslinking which enables the production of substantially only microgel<br />
particles, <strong>and</strong> the high shear of the process prevents undue growth of the<br />
microgels <strong>and</strong> enables the microgel particles to be uniformly distributed in<br />
the resin.<br />
20.3.4 Toner Resins with Low Fix Temperature<br />
Toners made from vinyl-type binder resins, such as styrene-acrylic resins,<br />
may cause a problem which is addressed as vinyl offset. Vinyl offset occurs<br />
when a sheet of paper or transparency with a fixed toner image is contacted,<br />
for a period of time, with a polyvinyl chloride surface containing a<br />
plasticizer used in making the vinyl material flexible such as, for example,<br />
in vinyl binder covers, <strong>and</strong> the fixed image adheres to the PVC surface.<br />
Crosslinked thermoplastic binder resins can be used as toners which
Toners 699<br />
possess a low fix temperature <strong>and</strong> a high offset temperature, <strong>and</strong> which<br />
show a substantially minimized vinyl offset. The resin composition consists<br />
of a linear reactive base resin, an initiator, <strong>and</strong> a polyester with an<br />
amine functionality. 2 The linear unsaturated polyester base resin is prepared<br />
from unsaturated diacids, e.g., maleic acid or fumaric acid <strong>and</strong> diols,<br />
like propylene glycol or propoxylated bisphenol A. Particularly suitable is<br />
poly(propoxylated bisphenol A fumarate). An amine-containing polyester<br />
is prepared from propoxylated 4,4 ′ -isopropylidene bisphenol A, N-phenyldiethanolamine,<br />
<strong>and</strong> fumaric acid. A peroxide, such as tert-butyl hydroperoxide,<br />
is used as radical initiator. In general, peroxides that thermally<br />
decompose at higher temperatures are preferred so that the amine promoted<br />
decomposition is favored at the polymer melt processing temperatures.<br />
To disperse small amounts of the peroxide thoroughly in the resin,<br />
a 0.6% master batch in poly[4,4 ′ -isopropylidenebisphenyl bispropanol bisether/fumaric<br />
acid] is formed. The peroxide/polyester mixture can be extruded<br />
at 120°C without decomposition of the peroxide under these conditions.<br />
In larger scale reactions the initiator can be added to the extruder by<br />
direct injection. To this blend in a next step, the amine containing polyester<br />
is then blended in an extruder. The amine polyesters are added in amounts<br />
from 1% to about 10%.<br />
The polymers are crosslinked in the molten state under high shear<br />
conditions, producing substantially uniformly dispersed microgels of high<br />
crosslinking density, preferably using certain chemical initiators as crosslinking<br />
agents in an extruder.<br />
The amine of the polyester reacts with the initiator to form free radicals.<br />
The tert-butoxy radical reacts with a vinyl bond in the polymer backbone<br />
which subsequently forms a crosslink between polymer chains when<br />
it, in turn, reacts with another vinyl bond in the polymer backbone.<br />
The crosslinked resin produced in this way is a clean <strong>and</strong> non-toxic<br />
polymer mixture comprising crosslinked gel particles <strong>and</strong> a noncrosslinked<br />
portion.<br />
20.3.4.1 Fixing Performance of the Toner<br />
The fixing performance of a toner can be characterized as a function of the<br />
temperature. 2 The lowest temperature at which the toner adheres to the<br />
support medium is referred to as the cold offset temperature (COT). The<br />
maximum temperature at which the toner does not adhere to the fuser roll
700 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
is referred to as the hot offset temperature (HOT). When the fuser temperature<br />
exceeds HOT, some of the molten toner adheres to the fuser roll<br />
during fixing <strong>and</strong> is transferred to subsequent substrates containing developed<br />
images resulting, for example, in blurred images. This undesirable<br />
phenomenon is known as offsetting.<br />
Between the COT <strong>and</strong> HOT of the toner is the minimum fix temperature<br />
(MFT), which is the minimum temperature at which acceptable<br />
adhesion of the toner to the support medium occurs, as determined by, for<br />
example, a creasing test. The difference between MFT <strong>and</strong> HOT is referred<br />
to as the fusing latitude.<br />
20.3.5 Toners for Textile Printing<br />
The imaging of textiles <strong>and</strong> other materials using thermal transfer of sublimable<br />
dyes has been commercially practiced for more than 50 years. With<br />
the introduction of laser printers for use with personal computers, attempts<br />
were made with only limited success to incorporate thermal transfer sublimable<br />
dyes into toners to be used in these printers. The printers were<br />
intended to image in only one color, particularly black.<br />
However, when a toner was properly formulated for this application<br />
<strong>and</strong> a sublimable dye was incorporated into the toner, images could be<br />
formed which could then be thermally transferred by the application of<br />
sufficient heat to vaporize the dye.<br />
By this method, a single color image could be formed. Since many<br />
of these laser printers used replaceable cartridges to carry the toner to form<br />
the image in this electrophotographic process, several of these special thermal<br />
transfer toners could be installed in several cartridges, including toners<br />
containing the process color dyes for cyan, magenta, <strong>and</strong> yellow color<br />
imaging.<br />
Using a color separation program on a personal computer connected<br />
to such a laser printer, a skilled operator could effectively create a color<br />
separation of a full color image <strong>and</strong> print each separation by installing in<br />
turn the appropriate cartridge containing the indicated color: cyan, magenta,<br />
or yellow. By this method, an image containing the appropriate cyan,<br />
yellow <strong>and</strong> magenta thermal transfer dyes can be constructed stepwise. 9<br />
The requirements for toner materials for good textile performance,<br />
i.e., low initial modulus, <strong>and</strong> flexibility differ from the requirements for<br />
production of toner powders by grinding, i.e. brittleness. 10, 11 Toner com-
Toners 701<br />
positions for use in textile printing are available. 12<br />
20.4 CHARACTERIZATION OF TONERS<br />
The powder flow test is a direct determination of the amount of energy<br />
necessary to pull apart aggregates of cohesive particles in a specified time.<br />
The powder flow of a toner is an important aspect to consider in designing<br />
a toner because of the required performance in the electrophotographic<br />
process. 1<br />
The powder flow test allows for the evaluation of the flowability of<br />
the toner by measuring the amount of toner passing through a sieve during<br />
a preset time relative to the initial loading of toner on the sieve. The<br />
sieve is supported on a cantilever <strong>and</strong> is vibrated at a frequency of 60 Hz.<br />
The intensity (amplitude) of the vibration is controlled using a voltage adjustment.<br />
Generally, a free flowing material will tend to flow steadily <strong>and</strong><br />
consistently. Conversely, a non free-flowing material will tend to flow as<br />
agglomerated particles.<br />
The cohesiveness of the toner is also an important characteristic.<br />
The cohesiveness affects powder flow, the lower cohesion values being<br />
associated with higher powder flows.<br />
To measure the cohesiveness, a measured amount of toner is placed<br />
on a screen. Three screens of reducing size are placed in series so that the<br />
powder goes through increasingly smaller screens.<br />
REFERENCES<br />
1. B. P. Livengood, B. W. Baird, <strong>and</strong> G. P. Marshall. <strong>Reactive</strong> compatibilization<br />
of polymeric components such as siloxane polymers with toner resins. US<br />
Patent 6 544 710, assigned to Lexmark International, Inc. (Lexington, KY),<br />
April 8 2003.<br />
2. P. G. Odell, S. V. Drappel, <strong>and</strong> M. S. Hawkins. <strong>Reactive</strong> melt mixing processes.<br />
US Patent 6 114 076, assigned to Xerox Corporation (Stamford, CT),<br />
September 5 2000.<br />
3. K. A. Moffat, M. N. V. McDougall, R. Carlini, D. A. Hays, J. T. LeStrange,<br />
<strong>and</strong> P. J. Gerroir. Toner compositions comprising vinyl resin <strong>and</strong> poly<br />
(3,4-ethylenedioxythiophene). US Patent 6 689 527, assigned to Xerox Corporation<br />
(Stamford, CT), February 10 2004.<br />
4. S. M. Silence, E. J. Gutman, <strong>and</strong> T. R. Hoffend. Toner compositions. US<br />
Patent 6 680 153, assigned to Xerox Corporation (Stamford, CT), January 20<br />
2004.
702 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
5. Y. F. Duan <strong>and</strong> Q. Zhang. Preparation of suspension polymerized color toners<br />
<strong>and</strong> correlation between ingredients <strong>and</strong> rheological behavior. J. Imaging Sci.<br />
Technol., 48(1):6–9, January–February 2004.<br />
6. S. Kiatkamjornwong <strong>and</strong> P. Pomsanam. Synthesis <strong>and</strong> characterization of<br />
styrenic-based polymerized toner <strong>and</strong> its composite for electrophotographic<br />
printing. J. Appl. Polym. Sci., 89(1):238–248, July 2003.<br />
7. J. R. Combes, K. A. Moffat, <strong>and</strong> M. N. V. McDougall. Toner compositions<br />
comprising polyester resin <strong>and</strong> polypyrrole. US Patent 6 743 559, assigned<br />
to Xerox Corporation (Stamford, CT), June 1 2004.<br />
8. K. A. Moffat, R. Carlini, M. N. V. McDougall, D. A. Hays, <strong>and</strong> J. T.<br />
LeStrange. Toner compositions comprising polyester resin <strong>and</strong> poly (3,4-ethylenedioxythiophene).<br />
US Patent 6 730 450, assigned to Xerox Corporation<br />
(Stamford, CT), May 4 2004.<br />
9. R. J. Thompson. Color toner containing sublimation dyes for use in electrophotographic<br />
imaging devices. US Patent 6 270 933, assigned to International<br />
Communication Materials, Inc. (Connellsville, PA), August 7 2001.<br />
10. W. W. Carr, D. S. Sarma, L. Cook, S. Shi, L. Wang, <strong>and</strong> P. H. Pfromm.<br />
Xerographic printing of textiles: Polymeric toners <strong>and</strong> their performance. J.<br />
Appl. Polym. Sci., 78(14):2425–2434, December 2000.<br />
11. W. W. Carr, F. L. Cook, H. Yan, <strong>and</strong> P. H. Pfromm. Application of dimer<br />
acid-based polyamide for xerographic toners for textiles printing. J. Appl.<br />
Polym. Sci., 81(10):2399–2407, September 2001.<br />
12. A. Verhecken <strong>and</strong> P. Sterckx. Toner composition for use in textile printing.<br />
US Patent 6 007 955, assigned to Agfa-Gevaert, N.V. (Mortsel, BE), December<br />
28 1999.
Index<br />
ACRONYMS<br />
AA<br />
Acrylic acid, 547, 647<br />
Ascorbic acid, 120<br />
ABS<br />
Acrylonitrile butadiene styrene, 213<br />
ACH<br />
Acetone cyanhydrin, 352<br />
ACP<br />
Amorphous calcium phosphates, 681<br />
AEP<br />
1-(2-Aminoethyl)piperazine, 563<br />
AIBN<br />
2,2 ′ -Azobis(isobutyronitrile), 601<br />
AKD<br />
Alkylketene dimer, 464<br />
AlN<br />
Aluminum nitride, 421<br />
ALS<br />
Alternating least squares, 196<br />
AMPC<br />
Allyl-N-(4-methyl-phenyl)carbamate, 570<br />
APS<br />
(3-Aminopropyl)triethoxysilane, 646<br />
ASA<br />
Alkenyl succinic anhydride, 464<br />
ATBC<br />
Acetyltributyl citrate, 366
704 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
ATBN<br />
Amine-terminated butadiene-acrylonitrile elastomers, 156<br />
ATPE<br />
Acid-group terminated poly(ethylene), 539<br />
ATR-FTIR<br />
Attenuated total reflectance Fourier transform infrared spectroscopy, 119,<br />
647<br />
ATRP<br />
Atom transfer radical polymerization, 82, 461, 568<br />
ATS<br />
(3-Aminopropyl)triethoxysilane, 205<br />
ATU<br />
Amine-terminated chain-extended urea, 156<br />
BAMPO<br />
Bis(m-aminophenyl)methylphosphine oxide, 169, 171, 176<br />
BAPP<br />
2,2-Bis[4-(4-aminophenoxy)phenyl]propane, 342<br />
Bis(4-aminophenoxy)phenylphosphine oxide, 169<br />
BAPPO<br />
Bis(4-aminophenyl)phenylphosphine oxide, 121, 172<br />
BAPQ<br />
2,3-Bis(4-(4-aminophenoxy)phenyl)quinoxaline-6-carboxylic acid, 412<br />
BAQ<br />
2,3-Bis(4-aminophenyl)quinoxaline-6-carboxylic acid, 412<br />
BCB<br />
Benzocyclobutene, 493<br />
BCBE<br />
1,2-Bis(benzocyclobutenyl)ethane, 493<br />
BD<br />
1,4-Butanediol, 119<br />
BDA<br />
1,4-Butane diamine, 121<br />
1,2-BDE<br />
1,4-Butanediol diglycidyl ether, 141, 205<br />
BDK<br />
2,2-Dimethoxy-1,2-diphenylethan-1-one, 193<br />
BDM<br />
4,4 ′ -Bis(maleimido)diphenylmethane, 418<br />
BDMA<br />
Benzyldimethylamine, 152<br />
BDMAEE<br />
Bis(2-dimethylaminoethyl)ether, 99, 103
Index 705<br />
BDMB<br />
2-Benzyl-2-dimethylamino-1-(4-morpholinophenyl)butan-1-one, 193<br />
BenzOXA<br />
Benzoxazole, 557<br />
BEPTPhS<br />
Bis(3-mercaptophenyl)sulfone, 208<br />
BET<br />
Brunauer Emmett Teller, 543<br />
BHET<br />
Bis(2-hydroxyethyl)terephthalate, 45<br />
BHMBE<br />
1,2-Bis-[2(2-hydroxy-5-methylphenyl)-5-benzotriazolyl]-ethane, 80<br />
BHMF<br />
Bis(hydroxymethyl)furan, 309<br />
BHT<br />
2,6-Di-tert-butyl-4-methylphenol, 677<br />
BIAE<br />
2-Bromoisobutyric acid ethylester, 570<br />
Bis-A-Dima<br />
Bisphenol A dimethacrylate, 660<br />
Bis-GMA<br />
2,2-Bis[4-(3-methacryloxy-2-hydroxypropoxy)phenyl]propane, 660<br />
Bis-M<br />
4,4 ′ -[1,3-Phenylene(1-methyl ethylidene)]bisaniline, 498<br />
BMDPM<br />
4,4 ′ -Bis(maleimido)diphenylmethane, 419<br />
BMI<br />
4,4 ′ -Bis(maleimido)diphenylmethane, 397<br />
4,4 ′ -Diphenylmethane bismaleimide, 547<br />
Bismaleimide, 387<br />
BMIE<br />
N,N-4,4-Diphenyl ether bismaleimide, 398<br />
Bis(4-maleimidophenyl)ether, 399<br />
BMIM<br />
4,4 ′ -Bis(maleimido)diphenylmethane, 398<br />
Bis(4-maleimidophenyl)methane, 399<br />
BMIP<br />
2,2-Bis[4-(4-maleimido phenoxy)phenyl]propane, 398, 399<br />
Bisphenol A bismaleimide, 398, 400<br />
BMIPO<br />
Bis(3-maleimidophenyl)phenylphosphine oxide, 402, 422<br />
BMIS<br />
Bis(4-maleimidophenyl)sulfone, 398, 399
706 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
BMPP<br />
2,2-Bis[4-(4-maleimido phenoxy)phenyl]propane, 434<br />
BMPPPO<br />
Bismaleimide(3,3 ′ -bis(maleimidophenyl))phenylphosphine oxide, 169, 171<br />
BOX<br />
2,2 ′ -(1,4-Phenylene)bisoxazoline, 547<br />
BP<br />
Benzophenone, 359, 629, 646<br />
BPFR<br />
Boric acid-modified phenolic resins, 257<br />
BPO<br />
Dibenzoyl peroxide, 568<br />
BT<br />
Bismaleimide triazine resins, 387<br />
CBC<br />
N,N ′ -Carbonylbiscaprolactam, 80<br />
CE<br />
Cyanate ester, 382<br />
CHO<br />
Cyclohexene oxide, 189<br />
CHP<br />
Cumene hydroperoxide, 244<br />
CMKGM<br />
Carboxymethyl konjac glucomannan, 121<br />
COT<br />
Cold offset temperature, 699<br />
CQ<br />
Camphorquinone, 673<br />
CR<br />
Controlled rheology, 588<br />
CTBN<br />
Carboxy-terminated butadiene/acrylonitrile copolymers, 156<br />
CTE<br />
Coefficient of thermal expansion, 421<br />
CXA<br />
Bis(1-oxyl-2,2,6,6-tetramethylpiperidine4-yl)sebacate, 602<br />
DA<br />
2,2 ′ -Pyromellitdiimidodisuccinic anhydride, 92<br />
Diels-Alder reaction, 309<br />
DAB<br />
1,4-Diaminobutane, 630<br />
DABCO<br />
1,4-Diazabicyclo[2.2.2]octane, 99
Index 707<br />
DAPB<br />
2,6-Di(4-aminophenoxy)benzonitrile, 417<br />
DAPNPT<br />
2,4-Di(2-allylphenoxy)-6-(2-naphthyloxy)-1,3,5-triazine, 417, 419<br />
DBA<br />
2,2 ′ -Diallyl bisphenol A, 164, 381, 382, 397, 398, 417, 418<br />
DBBA<br />
3,5-Di-tert-butyl-4-hydroxybenzyl acrylate, 632<br />
DBMX<br />
α,α ′ -Dibromo-m-xylene, 428<br />
DBTDL<br />
Dibutyltin dilaurate, 80, 107, 114, 567<br />
DBTO<br />
Dibutyltin oxide, 567<br />
DCDPT<br />
1,4-[Di(4-cyanato diphenyl-2,2 ′ -propane)]terephthalate, 387<br />
DCHE<br />
7,26-Dioxatrispirobicyclo[4.1.0]heptane-4,5 ′ -1,3-dioxane-2 ′ ,2 ′′ -<br />
1,3-dioxane-5 ′′ ,4 ′′ -bicyclo[4.1.0]heptane, 665, 667<br />
DCM<br />
4,4 ′ -Diamino-3,3 ′ -dimethyldicyclohexylmethane, 175<br />
DCP<br />
Dicumyl peroxide, 541, 609, 623, 629<br />
DD<br />
1,10-Decanediol, 117<br />
DDM<br />
4,4 ′ -Diaminodiphenylmethane, 402, 414, 423<br />
4,4 ′ -Methylenedianiline, 402<br />
DDS<br />
4,4 ′ -Diaminodiphenylsulfone, 153, 158, 175<br />
DEAEMA<br />
Diethylaminoethyl acrylate, 626<br />
Diethylaminoethyl methacrylate, 675<br />
DEGDA<br />
Diethylene glycol diacrylate, 638<br />
DEM<br />
Diethyl maleate, 542, 623<br />
DEPN<br />
N-tert-Butyl-1-diethylphosphono-2,2-dimethylpropyl nitroxide, 603<br />
DEPT NMR<br />
Distortionless enhancement by polarization transfer nuclear magnetic<br />
resonance spectroscopy, 293
708 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
DGDPI<br />
1,3-[Di(4-glycidyloxy diphenyl-2,2 ′ -propane)]isophthalate, 387<br />
DGEBA<br />
Bisphenol A diglycidyl ether, 139<br />
Diglycidyl ether of bisphenol A , 150<br />
DGEBTF<br />
Adduct of 2-chlorobenzotrifluoride <strong>and</strong> glycerol diglycidyl ether, 150<br />
DHBP<br />
2,5-Dimethyl-2,5-di(tert-butylperoxy)hexane, 516, 546, 591<br />
DHPDOPO<br />
10-(2,5-Dihydroxyphenyl)-9,10-dihydro-9-oxa-10-phosphaphenanthrene-10-oxide,<br />
169<br />
DICY<br />
Dicy<strong>and</strong>iamide, 402<br />
DMAA<br />
N,N-Dimethylacrylamide, 647<br />
DMAB<br />
2,4-Diamino-4 ′ -methylazobenzene, 176<br />
4-Dimethylaminobenzoin, 193<br />
3-DMABA<br />
3-Dimethylaminobenzoic acid, 193<br />
4-DMABA<br />
4-Dimethylaminobenzoic acid, 193<br />
DMABAL<br />
4-Dimethylaminobenzaldehyde, 193<br />
DMAEMA<br />
2-(Dimethylamino)ethyl methacrylate, 82<br />
DMAMP<br />
2-(Dimethylamino)-2-(hydroxymethyl)-1,3-propanediol, 265<br />
DMBA<br />
4-Dimethylamino-1-butanol, 119<br />
Dimethylol butanoic acid, 93, 121<br />
DMCDA<br />
5-(2,5-Dioxotetrahydrofuryl)-3-methyl-3-cyclohexene-1,2-dicarboxylic<br />
anhydride, 180<br />
DMEA<br />
N,N-Dimethylethylethanolamine, 119<br />
DMPA<br />
2,2-Dimethoxy-2-phenylacetophenone, 359<br />
Dimethylol propionic acid, 120<br />
DMPT<br />
N,N-Dimethyl-p-toluidine, 669
Index 709<br />
DMT<br />
Dimethyl terephthalate, 35<br />
DMTA<br />
2-Dimethylamino-2-methyl-1-propanol, 264<br />
DNS-EDA<br />
5-Dimethylaminonaphthalene-1-(2-aminoethyl)sulfonamide, 197<br />
DOPO<br />
9,10-Dihydro-9-oxa-10-phosphaphenanthrene-10-oxide, 112, 168, 169,<br />
405, 422<br />
DPD<br />
p-Phenyl diamine, 400<br />
DPHS<br />
Bis(3-diethylphosphono-4-hydroxyphenyl)sulfide, 169<br />
DSC<br />
Differential scanning calorimetry, 43, 114, 623<br />
DSC-SSA<br />
Differential scanning calorimetry-successive self-nucleation <strong>and</strong> annealing,<br />
631<br />
DSDA<br />
3,3 ′ ,4,4 ′ -Diphenylsulfone tetracarboxylic dianhydride, 342<br />
DTBP<br />
Di-tert-butyl peroxide, 591<br />
DVB-BCB<br />
Bis(benzocyclobutenyl)-m-divinylbenzene, 502<br />
DVS-BCB<br />
Bis(benzocyclobutenyl)divinyltetramethylsiloxane, 502<br />
DYBP<br />
2,5-Dimethyl-2,5-di(tert-butylperoxy)-3-hexyne, 516<br />
E-BCB<br />
1,2-Bis(4-benzocyclobutenyl)ethylene, 502<br />
e-EPDM<br />
Epoxidized ethylene propylene diene, 212<br />
E/EA<br />
Ethene/ethyl acrylate copolymer, 214<br />
EAA<br />
Ethylene-co-acrylic acid, 555<br />
Ethylene/acrylic acid copolymers, 213, 549<br />
EBPDMA<br />
Ethoxylated bisphenol A dimethacrylate, 660<br />
EBS<br />
N,N ′ -Ethylene-bisstearamide, 513<br />
EDA<br />
Ethylene diamine, 93, 121
710 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
EDMAB<br />
Ethyl-4-dimethylamino benzoate, 193, 669, 673, 675<br />
EG<br />
Ethylene glycol, 117<br />
Exp<strong>and</strong>able graphite, 112<br />
EGMA<br />
Ethylene/glycidylmethacrylate copolymer, 213, 540<br />
Poly(ethylene-co-glycidyl methacrylate), 552<br />
EHMOXA<br />
Ethyl hydroxymethyl oxazoline, 557<br />
EO<br />
Ethylene oxide, 571<br />
EPDM<br />
Ethylene propylene diene monomer, 606, 632<br />
EPIDA<br />
((3-(4-(1-(4-(3-(Bis-carboxymethylamino) 2-hydroxy-propoxy)<br />
phenyl)-1-methyl-ethyl) phenoxy) 2-hydroxypropyl) carboxy<br />
methylamino) acetic acid, 123<br />
EPN<br />
Epoxy-novolak, 416<br />
EPPHAA<br />
1,2-Epoxy-3-phenoxypropane, 159<br />
EPR<br />
Ethylene/propylene rubber, 557, 606, 632<br />
EPR-g-GMA<br />
Ethylene/propylene rubber grafted with GMA, 540<br />
EPR-g-MA<br />
Ethylene/propylene rubber grafted with maleic anhydride, 564<br />
EVA<br />
Ethylene/vinyl acetate, 153, 456<br />
EVALSH<br />
Mercapto-modified EVA, 560<br />
EY<br />
Elastic modulus, 680<br />
12F-PEK<br />
Fluorinated poly(aryl ether ketone), 160<br />
FA<br />
Furfuryl alcohol, 307, 312<br />
6FDA<br />
Hexafluoropropylidenebisphthalic dianhydride, 342<br />
FP<br />
Ratio of formaldehyde to phenol, 270
FPC<br />
Flexible printed circuits, 412<br />
FS<br />
Flexural strength, 680<br />
FTIR<br />
Fourier-transform infrared (spectroscopy), 114<br />
GLYMO<br />
3-Glycidoxypropyltrimethoxysilane, 205, 326<br />
GMA<br />
Glycidyl methacrylate, 141, 213, 635, 648, 660, 661<br />
GPC<br />
Gel permeation chromatography, 525<br />
GPE<br />
Glycidyl phenyl ether, 186<br />
GPN<br />
General-purpose novolak resins, 242<br />
GTL<br />
Glycol trilinoleate, 638<br />
H3M<br />
Hexa(methoxymethyl)melamine, 263<br />
HAB<br />
3,3 ′ -Dihydroxy-4,4 ′ -diaminobiphenyl, 342<br />
HAP<br />
Hexa(allylamino)cyclotriphosphonitrile, 548<br />
HBA<br />
Hydroxybenzoic acid, 498<br />
HBP<br />
Hyperbranched polymers, 144<br />
HCPA<br />
4-Hydroxybutyl-2-chloro-2-phenylacetate, 570<br />
HD<br />
1,6-Hexanediol, 184<br />
Hydrazine monohydrate, 121<br />
HDDMA<br />
1,6-Hexanediol dimethacrylate, 660<br />
HDI<br />
1,6-Hexane diisocyanate, 75<br />
HDPE<br />
High density poly(ethylene), 542<br />
HEMA<br />
2-Hydroxyethyl methacrylate, 123, 351, 518<br />
HEMAN<br />
Hydroxyethyl methacrylate maleic anhydride adduct, 660<br />
Index 711
712 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
HHPA<br />
Hexahydrophthalic anhydride, 163<br />
HIPS<br />
High impact poly(styrene), 536<br />
HMDI<br />
4,4-Methylene biscyclohexyl diisocyanate, 73<br />
HME<br />
Hexafunctional methacrylate ester, 660<br />
HMF<br />
5-Hydroxymethylfurfural, 308, 309<br />
HMTA<br />
Hexamethylenetetramine, 263, 264<br />
HNA<br />
Hydroxynaphthoic acid, 498<br />
HON<br />
High ortho novolak resins, 242<br />
HOT<br />
Hot offset temperature, 700<br />
HPA<br />
2-Hydroxypropyl acrylate, 20<br />
HPM<br />
N-(4-Hydroxyphenyl)maleimide, 402, 416<br />
HPN<br />
High para novolak resins, 242<br />
HQ<br />
Hydroquinone, 498<br />
HR<br />
Resiliency foams, 107<br />
HTEP<br />
(6-Hydroxy)hexyl-2-(trimethylaminonio)ethyl phosphate, 119<br />
HTPDMS<br />
Hydroxy-terminated poly(dimethylsiloxane), 414<br />
IA<br />
Itaconic acid, 620, 629<br />
IC<br />
Integrated circuites, 421<br />
IEM<br />
2-Isocyanatoethyl methacrylate, 351, 660<br />
IFSS<br />
Interfacial shear strength, 434<br />
IPDI<br />
Isophorone diisocyanate, 75
Index 713<br />
IPN<br />
Interpenetrating polymer network, 382<br />
IPO<br />
2-Isopropenyl-2-oxazoline, 573, 630<br />
IPP<br />
Isotactic poly(propylene), 547<br />
IPPA<br />
Poly(2,2-di(4-phenylene)propane phthalate-co-2,2-di(4-phenylene)propane<br />
isophthalate), 390<br />
IR<br />
Isoprene rubber, 632<br />
KCD<br />
3-Ketocoumarin, 209<br />
Kevlar<br />
Poly(p-phenylene terephthalamide), 563<br />
LC<br />
Liquid cristalline, 146<br />
Liquid crystal, 208<br />
LCDs<br />
Liquid crystal displays, 208<br />
LCGIC<br />
Light curable glass-ionomer cements, 663<br />
LCP<br />
Liquid crystalline polymers, 549<br />
LDI<br />
Lysine-diisocyanate, 120<br />
LDPE<br />
Low density poly(ethylene), 213, 542, 612, 620<br />
LEC<br />
Light-emitting electrochemical cell, 123<br />
LLDPE<br />
Linear low density poly(ethylene), 542, 635<br />
LOI<br />
Limiting oxygen index, 405, 501<br />
LPA<br />
Low-profile additives, 26<br />
MA<br />
Maleic anhydride, 521, 541, 612, 637<br />
Myristic acid, 366<br />
MA-g-PP<br />
Maleic anhydride-grafted-poly(propylene), 563<br />
MAC-10<br />
11-Methacryloyloxy-1,1-undecanedicarboxylic acid, 671
714 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
MBA<br />
Methacryloyl-β-alanine, 660, 663<br />
MBL<br />
α-Methylene-γ-butyrolactone, 665<br />
MCDEA<br />
4,4 ′ -Methylene bis(3-chloro-2,6-diethylaniline), 158<br />
MDA<br />
4,4 ′ -Methylenedianiline, 158, 175<br />
MDEA<br />
Methyldiethanolamine, 359<br />
MDI<br />
p,p ′ -Methylene diphenyl diisocyanate, 113<br />
Diphenylmethane diisocyanate, 74<br />
MDP-BMI<br />
1,1 ′ -(Methylene di-4,1-phenylene)bismaleimide, 423<br />
MDPE<br />
Medium density poly(ethylene), 539<br />
MEHQ<br />
Hydroquinone monomethyl ether, 677<br />
MeTHPA<br />
3-Methyl-1,2,3,6-tetrahydrophthalic anhydride, 180<br />
MF<br />
Melamine/formaldehyde, 303<br />
MFI<br />
Melt flow index, 587<br />
MFN<br />
Melt flow number, 587<br />
MFR<br />
Melt flow rate, 587<br />
MFT<br />
Minimum fix temperature, 700<br />
MKEA<br />
4,4-Bis(N,N-dimethyl-N-(2-ethoxycarbonyl-1-propenyl)ammonium<br />
hexafluoro antimonate)benzophenone, 189–191<br />
MMA<br />
Methyl methacrylate, 634<br />
MMT<br />
Montmorillonite, 20<br />
MOPIP<br />
1-(2-Methoxyphenyl)piperazine, 116<br />
MPD<br />
2-Methyl-1,3-propanediol, 14
Index 715<br />
MPDA<br />
m-Phenylene diamine, 272<br />
MPGE<br />
4-(N-Maleimidophenyl)glycidyl ether, 398, 402, 404<br />
MPS<br />
Maleic anhydride grafted poly(styrene), 637<br />
Mercaptopropyltrimethoxysilane, 343<br />
MPTMS<br />
3-Methacryloxypropoxytrimethoxysilane, 681<br />
MPTS<br />
3-Methacryloxypropyl-trimethoxysilane, 351, 365<br />
MWD<br />
Molecular weight distribution, 608<br />
NBR<br />
Acrylonitrile-butadiene, 53<br />
Nitrile rubber, 540<br />
NHCPA<br />
N-(2-Hydroxyethyl)-2-chloro-2-phenylacetamide, 570<br />
NLO<br />
Nonlinear optical, 209<br />
1 H-NMR<br />
Proton nuclear magnetic resonance spectroscopy, 140<br />
NPG<br />
N-Phenylglycine, 193<br />
NT-D<br />
1-(α-Naphthyl)-3,3-di(2-hydroxyethyl)-triazene-1, 93<br />
OCDI<br />
4,4 ′ -Diphenylmethane carbodiimide, 547<br />
ODOPB<br />
2-(6-Oxid-6H-dibenz[c,e][1,2]oxa-phosphorin-6-yl)-1,4-benzenediol, 168<br />
ODOPM<br />
2-(6-Oxid-6H-dibenz[c,e][1,2]oxaphosphorin-6-yl)methanol, 168<br />
ODPA<br />
4,4 ′ -Oxydiphthalic anhydride, 498<br />
OMT<br />
Organophilic montmorillonite, 111<br />
OPIA<br />
(4-Octyloxyphenyl)phenyliodonium hexafluoroantimonate, 192<br />
OPP<br />
Oriented poly(propylene), 460<br />
OXA<br />
Ricinoloxazoline maleate, 634
716 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
PA<br />
Polyamide, 463<br />
PA6<br />
Poly(ε-caprolactam), 550<br />
Polyamide 6, 213, 629<br />
PAI<br />
Polyamide-imide, 419<br />
PAVE<br />
Perfluoro (alkyl vinyl ether), 467<br />
PBA<br />
Pentabromobenzyl acrylate, 501<br />
PBO<br />
2,2 ′ -(1,3-Phenylene)bis(2-oxazoline), 564<br />
PBT<br />
Poly(benzo[1,2-d4,5-d ′ ]bisthiazole-2,6-diyl)-1,4-phenylene, 495<br />
Poly(butylene terephthalate), 214, 525, 541<br />
PBZT<br />
Poly(p-phenylene benzobisthiazole), 498<br />
PCB<br />
Printed circuit board, 378<br />
PCDMA<br />
Poly(carbonate)dimethacrylate, 660<br />
PCL<br />
Poly(ε-caprolactone), 517<br />
PDClPO<br />
Poly(2,6-dichloro-1,4-phenylene oxide), 555<br />
PDS<br />
Polydioxanone, 488<br />
PE-g-MA<br />
Poly(ethylene) grafted with maleic anhydride, 549<br />
PECH<br />
Poly(epichlorohydrin), 111, 112<br />
PEEK<br />
Poly(ether ether ketone), 154<br />
PEEK<br />
Poly(ether ether ketone), 418<br />
PEEK-C<br />
Phenolphthalein poly(ether ether ketone), 155<br />
PEEK-T<br />
Poly(ether ether ketone) based on tertiary butyl hydroquinone, 155<br />
PEG<br />
Poly(ethylene glycol), 400
Index 717<br />
PEG-MA<br />
Poly(ethylene glycol)methacrylate, 518<br />
PEG-PDMS<br />
Block copolymer of poly(ethylene glycol) <strong>and</strong> poly(dimethylsiloxane), 643<br />
PEGDMA<br />
Poly(ethylene glycol)dimethacrylate, 662<br />
PEI<br />
Polyetherimide, 417<br />
PEN<br />
Poly(ethylene 2,6-naphthalate), 555<br />
PEO<br />
Poly(ethylene oxide), 153, 206, 533<br />
Poly(ethylene-octene) copolymer, 551<br />
PET<br />
Poly(ethylene terephthalate), 342, 540<br />
PETA<br />
Pentaerythritol triacrylate, 516<br />
PF<br />
Phenol/formaldehyde (resin), 242<br />
PFS<br />
Phenol/formaldehyde sulfonate, 274<br />
PG<br />
Propylene glycol, 366<br />
PGA<br />
Polyglycolic acid, 488<br />
PGE<br />
Phenyl glycidyl ether, 142<br />
PHB<br />
Poly(p-hydroxybenzoate), 555<br />
PHBV<br />
Poly(β-hydroxybutyrate-co-β-hydroxyvalerate), 517<br />
PL<br />
β-Propiolactone, 119<br />
PLA<br />
Poly(lactide), 521<br />
Polylactic acid, 488, 519<br />
PLE<br />
Photopolymerizable liquid encapsulants, 211<br />
PMDA<br />
Pyromellitic dianhydride, 180, 524<br />
PMMA<br />
Poly(methyl methacrylate), 153, 533
718 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
PO<br />
Propylene oxide, 571<br />
POSS<br />
Polyhedral oligomeric silsesquioxane, 680<br />
PP<br />
Poly(propylene), 607, 617<br />
PP-g-MA<br />
Maleated poly(propylene), 541<br />
PPA<br />
Poly(2,2-di(4-phenylene)propane phthalate), 390<br />
PPDE<br />
Poly(phthaloyl diphenyl ether), 418<br />
PPE<br />
Poly(2,6-dimethyl-1,4-phenylene ether), 565<br />
Poly(phenylene ether), 214, 463<br />
Poly(phenylene ether)s, 564<br />
PPG<br />
Polyoxypropylene glycol, 390<br />
PPIDE<br />
Poly(phthaloyl diphenyl ether-co-isophthaloyl diphenyl ether), 418<br />
PPO<br />
Poly(2,6-dimethyl-1,4-phenylene oxide), 549, 555<br />
PPOH<br />
3-Phenyl-1-propanol, 567<br />
PPS<br />
Poly(phenylene sulfide), 559<br />
PPTDE<br />
Phthaloyl diphenyl ether-co-terephthaloyl diphenyl ether, 418<br />
PPV<br />
Poly(p-phenylene vinylene), 124<br />
PPy<br />
Poly(pyrrole), 161<br />
PROXYL<br />
2,2,5,5-Tetramethyl-1-pyrrolidinyloxy, 602<br />
PS<br />
1,3-Propanesulfone, 119<br />
Poly(styrene), 152, 557<br />
PSA<br />
Pressure-sensitive adhesives, 82, 460<br />
PSC<br />
1-Pyrenesulfonyl chloride, 196<br />
PT<br />
Phenolic cyanate/phenolic triazine copolymer, 386
Poly(thiophene), 645<br />
PT-D<br />
1-Phenyl-3,3-di(2-hydroxyethyl)-triazene-1, 93<br />
PTFE<br />
Poly(tetrafluoroethylene), 647<br />
PTMEG<br />
Poly(tetramethylene ether), 513<br />
PTMG<br />
Polytetramethylene glycol, 119<br />
PTT<br />
Poly(trimethylene terephthalate), 536<br />
PU<br />
Polyurethane, 69<br />
PU/PAN<br />
Polyurethane/polyacrylonitrile, 117<br />
PUA<br />
Polyurethane-acrylate, 116<br />
PUDMA<br />
Polyurethane dimethacrylate, 659, 660<br />
PUE<br />
Polyurethane elastomer, 111<br />
PVC<br />
Poly(vinyl chloride), 98<br />
PVDF<br />
Poly(vinylidene fluoride), 561<br />
PVDH<br />
Poly(vinylidene difluoride-co-hexafluoropropylene), 435<br />
QA<br />
N,N ′ -(4-Aminophenyl)-p-benzoquinone diimine, 400<br />
QDM<br />
o-Quinodimethane, 495<br />
re-HDPE<br />
Recycled high density poly(ethylene), 542<br />
REC<br />
Rectorite, 109<br />
RIE<br />
<strong>Reactive</strong> ion etching, 504<br />
RMGICs<br />
Resin-modified glass ionomer cements, 663<br />
RTD<br />
Residence time distribution, 514<br />
RTM<br />
Resin transfer molding, 400<br />
Index 719
720 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
S-g-PMA<br />
Starch graft poly(methyl acrylate), 639<br />
s-PS<br />
Syndiotactic poly(styrene), 212<br />
SAN<br />
Poly(styrene-co-acrylonitrile), 153<br />
Styrene/acrylonitrile copolymers, 214<br />
SAXS<br />
Small-angle X-ray scattering, 314<br />
SBR<br />
Styrene butadiene rubber, 465, 632<br />
SDS<br />
Sodium dodecyl sulfate, 644<br />
SEB<br />
Poly(styrene-b-(ethylene-co-butylene)), 542<br />
SEBS<br />
Styrene-b-(ethylene-co-1-butene)-b-styrene triblock copolymer, 542<br />
SEBS-g-MA<br />
Styrene-ethylene/butylene-styrene triblock copolymer, 541<br />
SEM<br />
Scanning electron microscopy, 551<br />
SG<br />
Styrene/glycidyl methacrylate, 212<br />
SiOC<br />
Silicon oxycarbide, 338<br />
SIPO<br />
2-Isopropenyl-2-oxazoline, 573<br />
SIS<br />
Poly(styrene-b-isoprene-b-styrene), 461<br />
SMA<br />
Styrene/maleic anhydride copolymer, 549, 630, 635<br />
SOC<br />
Spiroorthocarbonates, 665<br />
SOE<br />
Spiroorthoesters, 665<br />
SPE<br />
Solid polymer electrolytes, 122<br />
SSO<br />
Silsesquioxane, 199<br />
SUS<br />
10-Undecenyl sulfate, 644<br />
TA<br />
Tartaric acid, 120
TAA<br />
Tris(2-aminoethyl)amine, 484<br />
TAIC<br />
Triallyl isocyanurate, 211<br />
TAP<br />
Tris(2-allylphenoxy)triphenoxy cyclotriphosphazene, 435<br />
TAT<br />
Tris(2-allylphenoxy)-s-triazine, 435<br />
TBAEMA<br />
Diethylaminoethyl acrylate, 627<br />
TBBPA<br />
2,6,2 ′ ,6 ′ -Tetrabromobisphenol A, 32<br />
Tetrabromobisphenol A, 3<br />
TBPA<br />
Tetrabutylphosphonium acetate, 515<br />
TCDM<br />
Tetrahydrofurfuryl cyclohexene dimethacrylate, 660<br />
TDI<br />
Toluene diisocyanate, 73, 407<br />
TDS<br />
Transdermal delivery system, 366<br />
TEA<br />
Triethylamine, 121, 264<br />
TEC<br />
Triethyl citrate, 366<br />
TEGDI<br />
1,2-Bis(isocyanate)ethoxyethane, 73<br />
TEGDMA<br />
Triethylene glycol dimethacrylate, 659, 660, 675<br />
TEMPO<br />
2,2,6,6-Tetramethyl-1-piperidinyloxy, 603, 643<br />
Tetramethyl-1-piperidinyloxy, 568<br />
TEMPO<br />
2,2,6,6-Tetramethyl-1-piperidinyloxy, 602<br />
TEOS<br />
Tetraethoxysilane, 167, 325<br />
TFE<br />
Tetrafluoroethylene, 467<br />
TGDDM<br />
Tetraglycidyl diaminodiphenylmethane, 524<br />
Tetraglycidyl-4,4 ′ -diaminodiphenylmethane, 144, 153<br />
THF<br />
Tetrahydrofuran, 309<br />
Index 721
722 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
THFMA<br />
Tetrahydrofurfuryl methacrylate, 660<br />
TLCP<br />
Thermotropic liquid crystalline polymer, 553<br />
TMB<br />
1,2,4-Trimethoxybenzene, 193<br />
TMDSC<br />
Modulated differential scanning calorimetry, 194<br />
TME<br />
1,1,2,2-Tetramethoxyethane, 286<br />
TMI<br />
1-(Isopropenylphenyl)-1,1-dimethylmethyl isocyanate, 82<br />
3-Isopropenyl-α,α-dimethylbenzene isocyanate, 546<br />
TMPAE<br />
Trimethylolpropane mono allyl ether, 3<br />
TMPTA<br />
Trimethylolpropane triacrylate, 351, 513, 638<br />
TMPTMA<br />
1,1,1-Trimethylolpropane trimethacrylate, 660<br />
TMTEA<br />
Trimercaptotriethylamine, 208<br />
TOF-SIMS<br />
Time of flight single ion monitoring mass spectroscopy, 647<br />
TPA<br />
Terephthalic acid, 35<br />
TPGDA<br />
Tripropylene glycol diacrylate, 638<br />
TPMK<br />
2-Methyl-1-[4-(methylthio)phenyl]-2-morpholinopropan-1-one, 193<br />
TPP<br />
Triphenyl phosphite, 565<br />
TPPA<br />
Poly(2,2-di(4-phenylene)propane phthalate-co-2,2-di(4-phenylene)propane<br />
terephthalate), 390<br />
TPS<br />
Thermoplastic starch, 559<br />
TPT<br />
2,4,6-Triphenylpyrylium tetrafluoroborate, 485<br />
TPU<br />
Thermoplastic polyether polyurethanes, 122<br />
TRIS<br />
1,1,1-Trimethylolpropane triacrylate, 632
Index 723<br />
TSFA<br />
Triarylsulfonium hexafluoroantimonate, 208<br />
TTT<br />
Time-temperature-transition, 195<br />
UBMI<br />
Urethane-modified bismaleimide, 166<br />
UDMA<br />
1,6-Bis(methacryloxy-2-ethoxycarbonylamino)-2,4,4-trimethylhexane, 659<br />
Di-2-methacryloxyethyl-2,2,4-trimethylhexamethylenedicarbamate, 660<br />
Urethane dimethacrylate, 675<br />
UF<br />
Urea/formaldehyde, 11, 253, 286<br />
UHMF<br />
Ultra high melt flow, 605<br />
UHMWPE<br />
Ultra-high molecular weight poly(ethylene), 646<br />
UP<br />
Unsaturated polyester, 117<br />
VAc<br />
Vinyl acetate, 634<br />
VDAC<br />
Vinylbenzyldodecyldimethyl ammonium chloride, 20<br />
VEUH<br />
Vinylester-urethane hybrid resins, 212<br />
VOAC<br />
Vinylbenzyloctadecyldimethyl ammonium chloride, 20<br />
VOCs<br />
Volatile organic compounds, 11, 267, 311<br />
VTEOS<br />
Vinyltriethoxysilane, 631<br />
VTMS<br />
Vinyltrimethoxysilane, 631<br />
WOF<br />
Work of fracture, 680<br />
WPU<br />
Waterborne polyurethane, 121<br />
XPS<br />
X-ray photoelectron spectroscopy, 119, 645<br />
ZrDMA<br />
Zirconyl dimethacrylate, 681
724 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
CHEMICALS<br />
Abietic acid, 410, 411, 449<br />
Acetaldehyde, 243<br />
Acetic anhydride, 309, 407, 639<br />
Acetoacetoxy methyl methacrylate, 616<br />
Acetone cyanhydrin, 352<br />
Acetonitrile, 148<br />
2-Acetoxyethyl-dibutyltin, 108<br />
2-Acetoxyethyl-dibutyltin chloride, 108<br />
p-Acetoxystyrene, 182<br />
Acetylacetone peroxide, 36<br />
Acetyl chloride, 79<br />
Acetyl peroxide, 592<br />
Acetyltributyl citrate, 366<br />
Acrolein, 349, 352<br />
Acrylamide, 290, 369, 523, 648<br />
Acrylic acid, 11, 91, 119, 151, 290, 350, 351, 547, 551, 560, 645–647<br />
Acrylonitrile, 87, 104, 645<br />
Acryloyl-β-alanine, 660<br />
Acryloyl glutamic acid, 660<br />
Adipic Acid, 35<br />
Adipic acid, 3, 44, 89, 90<br />
Allo-ocimene, 449<br />
Allyl acetoacetate, 678<br />
Allyl alcohol, 12<br />
Allyl alcohol propoxylate, 35<br />
Allyl-4-[(4-N-allyl-N-ethyl)aminophenylazo]-α-cyanocinnamate, 436<br />
Allylamine, 434<br />
Allyl bromide, 34<br />
Allyl chloride, 139, 150<br />
1-Allyl-2-cyanatobenzene, 373<br />
Allyl cyanoacrylate, 473<br />
Allyl-4-[(4-N,N-diallyl)aminophenylazo]-α-cyanocinnamate, 436<br />
Allyl glycidyl ether, 142, 199, 200, 205, 571<br />
7-Allyloxy-2-naphthol, 411<br />
2-Allylphenol, 391, 418, 419<br />
4-Allylphenol, 391<br />
Allylsuccinic anhydride, 671<br />
Aluminium(III)acetylacetonate, 381<br />
Aluminum bromide, 311<br />
Aluminum isopropoxide, 521<br />
Aluminum isopropyloxide, 182
Aluminum nitride, 421<br />
Aluminum tri-sec-butylate, 678<br />
Aluminum trichloride, 311<br />
4-Amino-benzocyclobutene, 498<br />
o-Aminobenzoic acid, 13<br />
N-2-Aminoethyl-3-aminopropyl-tris(2-ethylhexoxy)silane, 483<br />
N-Aminoethyl piperazine, 175, 177<br />
1-(2-Aminoethyl)piperazine, 563<br />
1,3-Aminoethylpropanediol, 557<br />
m-Aminophenol, 243<br />
o-Aminophenol, 557<br />
p-Aminophenol, 142<br />
N,N ′ -(4-Aminophenyl)-p-benzoquinone diimine, 400<br />
1-(3 ′ -Aminopropyl)imidazole, 99<br />
(3-Aminopropyl)triethoxysilane, 23, 110, 205, 316, 414, 646<br />
Ammonium polyphosphate, 32, 111, 112<br />
Ammonium sulfate, 311<br />
O,O-tert-Amyl-O-(2-ethylhexyl)monoperoxy carbonate, 596<br />
tert-Amyl hydroperoxide, 591<br />
Amylopectin, 639<br />
Amylose starch, 639<br />
tert-Amylperoxybenzoate, 36<br />
tert-Amylperoxy-2-ethylhexanoate, 596<br />
4-(tert-Amylperoxy)-4-methyl-2-pentanol, 591, 592<br />
tert-Amylperoxyneodecanoate, 596<br />
tert-Amylperoxypivalate, 596<br />
Anatase, 365<br />
Aniline, 74, 75<br />
9-Anthroic acid, 197<br />
Antimony trioxide, 25, 32, 34, 357, 378<br />
Ascorbic acid, 120, 334, 668, 669<br />
Atropine, 344<br />
2-Azabicyclo[2.2.1]heptane, 99, 100<br />
2,2 ′ -Azobis(2-acetoxy)propane, 557, 601<br />
2,2 ′ -Azobis(2-amidinopropane)hydrochloride, 369<br />
2,2 ′ -Azobis(cyclohexanenitrile), 601<br />
2,2 ′ -Azobis(2,4-dimethyl-4-methoxyvaleronitrile), 601<br />
2,2 ′ -Azobis(2,4-dimethylvaleronitrile), 359, 601, 641<br />
2,2 ′ -Azobis(2-ethylpropionitrile), 642<br />
2,2 ′ -Azobis(isobutyronitrile), 35, 359, 601, 641, 697<br />
2,2 ′ -Azobis(2-methylbutyronitrile), 35, 601<br />
Barbituric acid, 668–670<br />
Index 725
726 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Barium metaborate, 357<br />
Barium sulfate, 19<br />
Barium titanate, 23<br />
Benzenesulfonic acid, 324<br />
Benzil, 673<br />
Benzocyclobutene, 493<br />
1-Benzocyclobutenyl-1-bromoethyl ether, 495<br />
1-Benzocyclobutenyl-1-hydroxyethyl ether, 495<br />
1-Benzocyclobutenyl vinyl ether, 493, 495<br />
Benzoguanamine, 301<br />
Benzoic acid, 51<br />
Benzoic acid 2,2,6,6-tetramethyl-piperidin-1-oxyl-4-yl ester, 615<br />
Benzoin isobutyl ether, 673<br />
Benzoin methyl ether, 37, 673<br />
Benzoin phenyl ether, 673<br />
Benzophenone, 359, 629, 646, 673<br />
p-Benzoquinone, 17, 168, 367, 481, 623, 670<br />
Benzoxazole, 557<br />
Benzoyl chloride, 79<br />
Benzyldimethylamine, 152<br />
2-Benzyl-2-dimethylamino-1-(4-morpholinophenyl)butan-1-one, 193<br />
Benzyl methacrylate, 153<br />
1-Benzyl-5-phenylbarbituric acid, 669<br />
N-Benzylpyrazinium hexafluoroantimonate, 184<br />
N-Benzylquinoxalinium hexafluoroantimonate, 184<br />
Benzyl tetrahydrothiophenium hexafluoroantimonate, 184<br />
Benzyltrimethylammonium chloride, 205, 402<br />
Betulin, 449<br />
Bicumene, 627<br />
Bicyclo[4.2.0]octa-1,3,5-triene, 493<br />
Bis-p-aminocyclohexylmethane, 175<br />
2,5-Bis(aminomethyl)bicyclo[2.2.1]heptane di(methylisopropylketimine), 176<br />
1,2-Bis(aminomethyl)cyclobutane, 179<br />
Bisaminomethylcyclohexane, 175<br />
3,5-Bis(4-aminophenoxy)benzoic acid, 82<br />
Bis(4-aminophenoxy)phenylphosphine oxide, 169<br />
2,2-Bis[4-(4-aminophenoxy)phenyl]propane, 342<br />
2,3-Bis(4-(4-aminophenoxy)phenyl)quinoxaline-6-carboxylic acid, 412<br />
Bis(m-aminophenyl)methylphosphine oxide, 169, 171, 176<br />
Bis(3-aminophenyl)phenylphosphine oxide, 402<br />
Bis(4-aminophenyl)phenylphosphine oxide, 121, 172<br />
2,3-Bis(4-aminophenyl)quinoxaline-6-carboxylic acid, 412<br />
1,3-Bis(3-aminopropyl)tetramethyldisiloxane, 142
Index 727<br />
2,6-Bis-4-benzocyclobutene benzo[1,2-d:5,4-d ′ ]bisoxazole, 493, 496<br />
Bis(benzocyclobutenyl)-m-divinylbenzene, 502<br />
Bis(benzocyclobutenyl)divinyltetramethylsiloxane, 502<br />
1,2-Bis(benzocyclobutenyl)ethane, 493<br />
1,2-Bis(4-benzocyclobutenyl)ethylene, 502<br />
2,6-Bis(4-benzocyclobutenyloxy)benzonitrile, 493<br />
4,4 ′ -Bis(sec-Butylamine)dicyclohexylmethane, 93<br />
4,4 ′ -Bis(sec-Butylamine)diphenylmethane, 93<br />
Bis(4-tert-Butylcyclohexyl)peroxydicarbonate, 36, 359<br />
Bis(4-tert-butyl-1-isopropyl-2-imidazolyl)disulfide, 479<br />
α,α ′ -Bis(tert-butylperoxy)diisopropyl benzene, 597<br />
1,1-Bis(tert-butylperoxy)-3,3,5-trimethylcyclohexane, 51, 362<br />
((3-(4-(1-(4-(3-(Bis-carboxymethylamino) 2-hydroxy-propoxy)<br />
phenyl)-1-methyl-ethyl) phenoxy) 2-hydroxypropyl) carboxy<br />
methylamino) acetic acid, 123<br />
1,7-Bis(chlorotetramethyldisiloxy)-m-carborane, 336, 337<br />
Bis(4-cyanatocumyl)benzene cyanate, 374<br />
1,1-Bis(4-cyanatophenyl)ethane, 196, 377<br />
Bis(4-cyanatophenyl)ether, 377<br />
2,2-Bis(4-Cyanatophenyl)1,1,1,3,3,3-hexafluoropropane, 377<br />
Bis(4-cyanatophenyl)methane, 377<br />
1,3-Bis(4-cyanatophenyl-1-(1-methylethylidene))benzene, 377<br />
1,3-Bis(4-cyanatophenyl-1-(methylethylidene))benzene, 377<br />
2,2 ′ -Bis(4-cyanatophenyl)propane, 382<br />
2,2-Bis(4-cyanatophenyl)propane, 377, 388<br />
Bis(4-cyanatophenyl)thioether, 377<br />
1,3-Bis[2 ′ -cyano-3 ′ ,3-diphenylacryloyloxy]-<br />
2,2-bis-[[2-cyano-3 ′ ,3 ′ -diphenylacryloyloxy]methyl]propane, 683<br />
2,2-Bis(4,4-di-tert-butylperoxycyclohexyl)propane, 592<br />
Bis(2,6-dichlorobenzoyl)-(4-propylphenyl)phosphine oxide, 37, 39<br />
4,4 ′ -Bis(diethylamino)benzophenone, 193<br />
Bis(3-diethylphosphono-4-hydroxyphenyl)sulfide, 169<br />
Bis(2,6-dimethoxybenzoyl)-2,4,4-trimethylpentylphosphine oxide, 37<br />
4,4 ′ -Bis(dimethylamino)benzophenone, 189<br />
Bis(2-dimethylaminoethyl)ether, 99, 103<br />
N,N-Bis(3-dimethylamino-n-propyl)amine, 102<br />
Bis(3-(N,N-dimethylamino)propyl)amine, 99<br />
N,N-Bis(3-dimethylaminopropyl)formamide, 105<br />
N,N-Bis[3-(dimethylamino)propyl]formamide, 103<br />
N,N ′ -Bis(3-dimethylaminopropyl)urea, 105<br />
Bis(3,5-dimethyl-4-cyanatophenyl)methane, 377<br />
4,4-Bis(N,N-dimethyl-N-(2-ethoxycarbonyl-1-propenyl)ammonium hexafluoro<br />
antimonate)benzophenone, 187, 189–191
728 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Bis(dimethylsilyl)benzene, 335<br />
1,2-Bis(2,3-epoxycyclohexyloxy)propane, 202<br />
Bis(3,4-epoxy-6-methylcyclohexylmethyl)adipate, 141<br />
Bis[3-(2,3-epoxypropyl thio)phenyl]sulfone, 141<br />
Bis(3-glycidyloxy)phenylphosphine oxide, 169<br />
Bishydantoin, 142<br />
2,2-Bis(4-hydroxy-3,5-dibromophenyl)propane, 357<br />
Bis(2-hydroxy-3,5-dimethylbenzyl)ether, 260<br />
Bis(2-hydroxy-3,5-dimethyl-benzyl)methylene, 260<br />
Bis(2-hydroxyethyl)terephthalate, 45<br />
Bis(hydroxyethyl)-p-toluidine, 669<br />
2,2-Bis[p-(2-hydroxy-3-methacryloxypropoxy)phenyl]propane, 661<br />
4,4 ′ -Bis(2-hydroxy-3-methacryloylpropoxy)biphenyl, 664<br />
Bis(hydroxymethyl)furan, 309<br />
1,2-Bis-[2(2-hydroxy-5-methylphenyl)-5-benzotriazolyl]-ethane, 80<br />
2,2-Bis(4-hydroxyphenyl)butane, 243<br />
Bis(4-hydroxyphenyl)methane, 243<br />
2,2-Bis(4-hydroxyphenyl)propane, 243<br />
N,N ′ -Bis(2-hydroxypropylaniline), 93<br />
Bis[N-(3-imidazolidinylpropyl)]oxamide, 103<br />
1,2-Bis(isocyanate)ethoxyethane, 73<br />
Bismaleimide(3,3 ′ -bis(maleimidophenyl))phenylphosphine oxide, 169, 171<br />
1,3-Bis(maleimido)benzene, 414<br />
4,4 ′ -Bis(maleimido)diphenylmethane, 397, 398, 405, 407, 418, 419, 425<br />
1,3-Bis(maleimidomethyl)cyclohexane, 398, 414<br />
1,3-Bis(4-maleimido phenoxy)benzene, 400<br />
1,4-Bis(4-maleimido phenoxy)benzene, 400<br />
2,2-Bis[4-(4-maleimido phenoxy)phenyl]propane, 388, 398, 399, 434<br />
Bis(4-maleimidophenyl)ether, 399<br />
Bis(4-maleimidophenyl)methane, 399<br />
3,3 ′ -Bis(maleimidophenyl)phenylphosphine oxide, 402, 422<br />
Bis(3-maleimidophenyl)phenylphosphine oxide, 402, 422<br />
4,4 ′ -Bismaleimidophenylphosphonate, 398<br />
Bis(4-maleimidophenyl)sulfone, 398, 399<br />
Bis(3-mercaptophenyl)sulfone, 208<br />
1,6-Bis(methacryloxy-2-ethoxycarbonylamino)-2,4,4-trimethylhexane, 659<br />
2,2-Bis[4-(3-methacryloxy-2-hydroxypropoxy)phenyl]propane, 660<br />
2,2 ′ -Bis(α-methacryloxy-β-hydroxypropoxyphenyl)propane diphosphonate, 684<br />
Bis(2-methacryloyloxyethyl)hydrogen phosphate, 671<br />
Bis[2-(methacryloyloxy)ethyl]phosphate, 665<br />
1,1-Bis(3-methyl-4-cyanatophenyl)cyclohexane, 377<br />
Bis(1-methyl-imidazole)zinc(II)diacetyl-acetonate, 381<br />
Bis(1-methyl-imidazole)zinc(II)dicyanate, 381
Index 729<br />
Bis(1-methyl-imidazole)zinc(II)dioctoate, 381<br />
Bis-1,3-methyl-1,2,3,4,5-pentamethylcyclopenta-2,4-diene benzene, 429<br />
Bis(methyl salicyl)carbonate, 515<br />
Bis[N-(3-morpholinopropyl)]oxamide, 103<br />
Bismuth neodecanoate, 108<br />
Bis(4-nitrophenyl)phenylphosphine oxide, 121<br />
2,2-Bis(4-(oligo(ethoxy))phenyl)propane diacetate, 672<br />
2,2-Bis(4-(oligo(ethoxy))phenyl)propanedimethacrylate, 672<br />
Bis(1-oxyl-2,2,6,6-tetramethylpiperidine4-yl)sebacate, 602, 603<br />
Bisphenol A, 35, 142, 148, 150, 180, 243, 246, 514<br />
Bisphenol A bismaleimide, 398, 400<br />
Bisphenol A dicyanate, 381, 389, 390<br />
Bisphenol A diglycidyl ether, 139<br />
Bisphenol A diglycidyl ether dimethacrylate, 658<br />
Bisphenol A dimethacrylate, 660<br />
Bisphenol B, 243<br />
Bisphenol F, 142, 243<br />
4,4 ′ -Bis(o-propenylphenoxy)benzophenone, 417<br />
Bis(4-(1,2,4-triazoline-3,5-dione-4-yl)phenyl)methane, 410<br />
Bis(2,4,6-trimethylbenzoyl)phenylphosphine oxide, 52<br />
Bis(3,5,5-trimethylhexanoyl)peroxide, 359<br />
Boric acid, 101, 257, 321, 419<br />
Boric anhydride, 311<br />
Boron fluoride, 311<br />
Boron trifluoride, 183, 315, 453, 481<br />
1-Bromobenzocyclobutene, 495<br />
Butadiene diepoxide, 141<br />
1,4-Butane diamine, 121<br />
1,4-Butanediisocyanate, 120<br />
1,2-Butanediol, 44<br />
1,4-Butanediol, 35, 44, 52, 110, 113, 119, 142, 245, 291<br />
2,3-Butanediol, 44<br />
1,4-Butanediol diglycidyl ether, 141, 205<br />
1,3-Butanediol dimethacrylate, 662<br />
cis-2-Butene-1,4-diol, 5<br />
tert-Butyl acrylamide, 642<br />
n-Butyl acrylate, 26, 91, 345, 349, 351, 365, 538, 642, 697<br />
tert-Butyl acrylate, 569<br />
tert-Butyl alcohol, 186<br />
tert-Butyl catechol, 42, 481<br />
tert-Butylcumyl peroxide, 36<br />
n-Butyl cyanoacrylate, 473, 475<br />
N-tert-Butyl-1-dibenzylphosphono-2,2-dimethylpropyl nitroxide, 602
730 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
n-Butyl-4,4-di(tert-butylperoxy)valerate, 596<br />
N-tert-Butyl-1-diethylphosphono-2,2-dimethylpropyl nitroxide, 602, 603<br />
N-tert-Butyl[(1-diethylphosphono)-2-methyl-propyl]nitroxide, 602<br />
o-tert-Butyl-di-1-piperidinylphosphonamidate, 184, 186<br />
N-tert-Butyl-1-di(2,2,2-trifluoroethyl)phosphono-2,2-dimethylpropyl nitroxide,<br />
602<br />
Butylene oxide, 85<br />
O,O-tert-Butyl-O-(2-ethylhexyl)monoperoxy carbonate, 596<br />
tert-Butyl hydroperoxide, 36, 362, 591, 597, 699<br />
tert-Butyl hydroquinone, 481<br />
O,O-tert-Butyl-O-isopropyl monoperoxy carbonate, 596<br />
n-Butyl methacrylate, 351, 365, 637, 638<br />
tert-Butyl methacrylate, 569<br />
2-(3-tert-Butyl-5-methyl-2-hydroxyphenyl)-5-chlorobenzothiazole, 356<br />
N-tert-Butyl-1-(2-naphthyl)-2-methylpropyl nitroxide, 602<br />
tert-Butylperoxyacetate, 596<br />
tert-Butylperoxybenzoate, 28, 36, 40, 360, 362, 596, 597<br />
tert-Butylperoxy-2-ethylhexanoate, 36, 596<br />
tert-Butylperoxyisobutyrate, 596<br />
tert-Butylperoxyisononanoate, 596<br />
tert-Butylperoxymaleate, 596<br />
tert-Butylperoxyneodecanoate, 596<br />
tert-Butylperoxypivalate, 596, 641<br />
tert-Butylperoxy-3,5,5-trimethylhexanoate, 596<br />
N-tert-Butyl-1-phenyl-2-methylpropyl nitroxide, 602<br />
p-tert-Butylphenyl salicylate, 356<br />
Butyl stearate, 476<br />
n-Butyl vinyl ether, 190<br />
2-Butyne-1,4-diol, 5<br />
Butyraldehyde, 243<br />
γ-Butyrolactone, 264<br />
Calcium hydroxy apatite, 678<br />
Calcium stearate, 28, 589<br />
Calixarene, 187<br />
Camphene, 449<br />
Camphorquinone, 662, 673<br />
ε-Caprolactam, 80, 536, 546<br />
N,N ′ -Carbonylbiscaprolactam, 80<br />
Carboxymethyl chitin, 121<br />
Carboxymethyl konjac glucomannan, 121<br />
N-(p-Carboxyphenyl)maleimide, 200<br />
o-Carboxy phthalanilic acid, 3, 13<br />
3-Carboxy-2,2,5,5-tetramethyl-pyrrolidinyloxy, 602
Cardanol, 243<br />
Cardene, 493<br />
Cardol, 243<br />
Carene, 449, 452<br />
Carophyllene, 449<br />
β-Carotine, 449<br />
Casein, 121, 122<br />
Cassava starch, 545<br />
Catechol, 17, 481<br />
Celluloid, 658<br />
Cellulose, 545<br />
Cetyl pyridinium chloride, 695<br />
Chitosan, 118, 545<br />
Chloranil, 17<br />
Chloro acetic acid, 474<br />
Chlorobenzene, 324<br />
p-Chlorobenzoyl peroxide, 592<br />
4-Chloro-3,5-diamino-benzoic acid isobutylester, 93<br />
Chlorodibutyltin hydride, 108<br />
1-Chloro-2,3-epoxypropane, 139<br />
Chloroethyl diazoacetate, 631<br />
m-Chloroperbenzoic acid, 205<br />
Chloroplatinic acid, 333<br />
3-Chloro-1,2-propanediol, 111<br />
Chlorosulfonic acid, 434<br />
Choline octoate, 334<br />
Chrysanthemol, 449<br />
Cinnamic acid, 208<br />
Citric acid, 52, 311<br />
Cobalt acetylacetonate, 38<br />
Cobalt 2-ethylhexanoate, 360<br />
Cobalt(II)acetylacetonate, 381<br />
Cobalt octoate, 28, 38<br />
Copper phthalocyanine, 695<br />
Cornstarch, 248, 343, 639<br />
Creatinine, 636<br />
Creosote, 344<br />
m-Cresol, 243, 268<br />
o-Cresol, 168, 244, 275, 387<br />
p-Cresol, 243, 268<br />
Cumene hydroperoxide, 36, 244, 591, 671<br />
α-Cumylperoxyneodecanoate, 596<br />
Cupric oxide, 387<br />
Index 731
732 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Cuprous oxide, 387<br />
3-(2-Cyanatophenyl)propyltrimethoxysilane, 391<br />
3-(4-Cyanatophenyl)propyltrimethoxysilane, 391<br />
2-Cyanoacrylate, 480, 483<br />
2-Cyanoacrylic acid, 477<br />
4 ′ -Cyano-4-biphenyloxyvaleric acid, 663, 664<br />
Cyanoethylmethylaniline, 673<br />
Cyanogen bromide, 374<br />
Cyanuric chloride, 419<br />
Cyclobutabenzene, 493<br />
Cyclobutarene, 493<br />
1,4-Cyclohexane diamine, 93<br />
1,4-Cyclohexanedimethanol, 49, 154<br />
Cyclohexanone peroxide, 362<br />
Cyclohexene, 147<br />
Cyclohexene oxide, 189<br />
Cyclohexenoic acid, 201<br />
Cyclohexyl methacrylate, 350, 351<br />
2-Cyclohexyl-5-methylphenol, 243, 268<br />
Cyclopentylamine, 289<br />
Decabromodiphenyloxide, 31, 32<br />
Decalin, 632<br />
Decanedioic acid bis(2,2,6,6-tetramethyl-piperidin-1-oxyl-4-yl), 615<br />
1,10-Decanediol, 117<br />
Decanoyl peroxide, 592<br />
1-Decene, 147<br />
Diabietylketone, 410<br />
3,5-Diacetyl-1,4-dihydrolutidine, 284<br />
2,2 ′ -Diallyl bisphenol A, 164, 381, 382, 397, 398, 400, 417, 418, 424, 425, 427,<br />
428<br />
(4-(N,N-Diallyl)-4 ′ -nitrophenyl)azoaniline, 436, 437<br />
2,4-Di(2-allylphenoxy)-6-N,N-dimethylamino-1,3,5-triazine, 417, 419<br />
2,4-Di(2-allylphenoxy)-6-(2-naphthyloxy)-1,3,5-triazine, 417, 419, 420<br />
1,4-Diallyl phenyl ether, 400<br />
Diallyl phthalate, 8<br />
3,5-Diaminobenzoic acid, 109<br />
1,4-Diaminobutane, 630<br />
1,2-Diaminocyclohexane, 175<br />
4,4 ′ -Diaminodibenzyl, 80<br />
2,4-Diamino-3,5-diethyl toluene, 175<br />
2,6-Diamino-3,5-diethyl toluene, 175<br />
Diaminodiethyl toluene, 175<br />
4,4 ′ -Diamino-3,3 ′ -dimethyldicyclohexylmethane, 175
Index 733<br />
4,4 ′ -Diaminodiphenylmethane, 142, 163, 167, 175, 178, 196, 198, 402, 407, 414,<br />
423<br />
4,4 ′ -Diaminodiphenylsulfone, 153, 158, 163, 175, 176, 178, 198<br />
2,4-Diamino-4 ′ -methylazobenzene, 176<br />
2,6-Di(4-aminophenoxy)benzonitrile, 417<br />
3,5-Diaminophenyl-4-benzocyclobutenylketone, 498<br />
(N-4,6-Diamino-1,3,5-triazin-2-yl)-1,3,5-triazine-2,4,6-triamine, 299<br />
Diaminotricyclododecane, 179<br />
2-(3,5-Di-tert-amyl-2-hydroxyphenyl)benzotriazole, 356<br />
Di-tert-amyl peroxide, 592<br />
1,1-Di(tert-amylperoxy)cyclohexane, 592<br />
2,2-Di(tert-amyl)peroxypropane, 592<br />
1,5-Diazabicyclo[4.3.0]non-5-ene, 483<br />
1,4-Diazabicyclo[2.2.2]octane, 99–101<br />
1,8-Diazabicyclo[5.4.0]undec-7-ene, 483, 484<br />
1,5-Diazobicyclo[4.3.0]non-5-ene, 102<br />
1,5-Diazobicyclo[4.3.0]non-5-ene, 101<br />
1,8-Diazobicyclo[5.4.0]undec-7-ene, 101, 102<br />
o-Diazonaphthoquinone, 268<br />
1,2,5,6-Dibenzocyclooctadiene, 495<br />
Dibenzodiazyl disulfide, 479<br />
Dibenzoyl peroxide, 36, 40, 359, 486, 568, 592, 597, 668<br />
N,N-4,4-Dibenzylbismaleimide, 398, 412<br />
1,1-Dibromo-2,2-bis(4-cyanatophenyl)ethylene, 377<br />
Dibromoneopentylglycol, 34<br />
Dibromostyrene, 34<br />
α,α ′ -Dibromo-m-xylene, 428<br />
Dibutoxybis(acetylacetonato)titanium(IV), 421<br />
Di-tert-butyl fumarate, 571<br />
3,5-Di-tert-butyl-4-hydroxybenzyl acrylate, 632<br />
2-(3,5-Di-tert-butyl-2-hydroxyphenyl)benzotriazole, 356<br />
2-(3,5-Di-tert-Butyl-2-hydroxyphenyl)-5-chlorobenzothiazole, 356<br />
3,5-Di-tert-butyl-4-hydroxyphenyl-propanoic acid, 622<br />
2,6-Di-tert-butyl-4-methylphenol, 677<br />
Di-tert-butyl peroxide, 40, 591, 592<br />
2,2-Di(tert-butylperoxy)butane, 592<br />
1,1-Di(tert-butylperoxy)cyclohexane, 592<br />
1,1-Di-(tert-butylperoxy)cyclohexane, 698<br />
α,α ′ -Di(tert-butylperoxy)diisopropylbenzene, 557<br />
1,3-Di(2-tert-butylperoxyisopropyl)benzene, 597<br />
1,4-Di(tert-butylperoxyisopropyl)benzene, 592, 599<br />
Di(2-tert-butylperoxyisopropyl)benzene, 597<br />
1,1-Di(tert-butylperoxy)-3,3,5-trimethylcyclohexane, 51, 592, 638
734 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
o,o-Di-tert-Butyl phenylphosphonate, 184<br />
Dibutyl phosphite, 684<br />
Dibutyl phthalate, 475, 476<br />
o,o-Di-tert-butyl-1-piperidinylphosphonamidate, 184, 186<br />
1,3-Di-n-butyltetramethyldisilazane, 338<br />
1,3-Di-tert-butyltetramethyldisilazane, 338<br />
Dibutyltin bis(2,3-dihydroxypropylmercaptide), 107, 108<br />
Dibutyltin bis(4-hydroxyphenylacetate), 107, 108<br />
Dibutyltin diacetate, 107, 331<br />
Dibutyltin dilaurate, 80, 107, 108, 114, 381, 414, 567, 688<br />
Dibutyltin dilauryl mercaptide, 107<br />
Dibutyltin dimercaptide, 107<br />
Dibutyltin oxide, 184, 567, 697<br />
2,5-Dicarboxyaldehyde-furan, 309<br />
Dichloroacetic acid, 40<br />
Dichlorobenzaldehyde, 206<br />
1,1-Dichloro-2,2-bis(4-cyanatophenyl)ethylene, 377<br />
Dichlorobis(triphenylphosphine)platinum(II), 333<br />
Dichlorodimethylsilane, 343, 414<br />
Dichloroethane, 147<br />
Dichloromethane, 381, 434<br />
1,3-Dichlorotetramethyldisiloxane, 336, 337<br />
Dicumyl, 627<br />
Dicumyl hydroperoxide, 597<br />
Dicumyl peroxide, 36, 362, 541, 597, 609, 623, 629<br />
4,4-Dicyanatobiphenyl, 377<br />
1,4-[Di(4-cyanato diphenyl-2,2 ′ -propane)]terephthalate, 387<br />
Dicy<strong>and</strong>iamide, 176, 299, 300, 402<br />
Dicyclohexylmethane-4,4 ′ -diisocyanate, 73, 75<br />
Dicyclohexylperoxydicarbonate, 596<br />
o,o-Dicyclohexyl phenylphosphonate, 184<br />
Dicyclopentadiene, 6, 7, 35, 454<br />
Didodecyl fumarate, 52<br />
1,3-Didodecyloxy-2-glycidyl-glycerol, 141<br />
1,3-Diethenyl-1,1,3,3-tetramethyldisiloxane, 333<br />
2-(2-N,N-Diethylaminoethoxy)ethanol, 99, 105<br />
Diethylaminoethyl acrylate, 626, 627<br />
Diethylaminoethyl methacrylate, 675<br />
Diethylaminopropylamine, 175, 177<br />
Diethyl-2,2-dicyanoglutarate, 471<br />
Diethylene glycol, 3, 11, 15, 44, 89, 93, 103, 200, 697<br />
Diethylene glycol diacrylate, 638<br />
Diethylenetriamine, 87, 175, 177
Index 735<br />
Di(2-ethylhexyl)peroxydicarbonate, 596<br />
Di-2-ethylhexyl phosphate, 684<br />
Di-2-ethylhexyl phosphite, 684<br />
Diethylketone, 593<br />
Diethyl maleate, 542, 623<br />
Diethyl malonate, 80<br />
Diethyl sebacate, 476<br />
Diethylsuccinate, 536, 550<br />
2,4-Diethylthioxanthone, 188<br />
Diethyltoluene diamine, 93<br />
N,N-Diethyltoluidine, 479<br />
1,3-[Di(4-glycidyloxy diphenyl-2,2 ′ -propane)]isophthalate, 387<br />
Diglycidyl tetrahydrophthalate, 525<br />
1,3-Dihexyltetramethyldisilazane, 338<br />
1,2-Dihydrocyclobutabenzene-3,6-dicarboxylic acid, 493, 495, 496, 498<br />
9,10-Dihydro-9-oxa-10-phosphaphenanthrene-10-oxide, 112, 168, 169, 405, 422<br />
Dihydrophthalimide, 410<br />
1,4-Dihydroxybenzene, 622<br />
2,4-Dihydroxybenzophenone, 356, 683<br />
4,4 ′ -Dihydroxybiphenyl, 663<br />
4,4 ′ -Dihydroxychalcone, 208, 209<br />
3,3 ′ -Dihydroxy-4,4 ′ -diaminobiphenyl, 342<br />
2,2 ′ -Dihydroxy-4,4 ′ -dimethoxybenzophenone, 356<br />
1,4-Di(2-hydroxyethyl)hydroquinone, 93<br />
Dihydroxyethyl-p-toluidine, 666<br />
α,α ′ -Dihydroxyl-poly(butyl acrylate), 82<br />
2,2 ′ -Dihydroxy-4-methoxybenzophenone, 356<br />
2,7-Dihydroxynaphthalene dicyanate, 377<br />
10-(2,5-Dihydroxyphenyl)-9,10-dihydro-9-oxa-10-phosphaphenanthrene-10-oxide,<br />
169<br />
Diisobutyl aluminum hydride, 521<br />
1-Diisobutylene, 453<br />
2-Diisobutylene, 453<br />
4,4 ′ -Diisocyanato dicyclo hexylmethane, 73<br />
Diisopropylbenzene mono hydroperoxide, 591<br />
1,4-Dilithio-1,3-butadiyne, 336<br />
Di-2-methacryloxyethyl-2,2,4-trimethylhexamethylenedicarbamate, 660<br />
o,o ′ -Dimethallyl bisphenol A, 418<br />
3,9-Di(p-methoxybenzyl)-1,5,7,11-tetra-oxaspiro[5.5]undecane, 184, 185<br />
Dimethoxydiethoxysilane, 325<br />
2,2-Dimethoxy-1,2-diphenylethan-1-one, 193<br />
2,2-Dimethoxy-2-phenylacetophenone, 37, 359<br />
N,N-Dimethylacetamide, 412, 623
736 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
N,N-Dimethylacrylamide, 647<br />
Dimethylamine, 156, 419<br />
4-Dimethylaminobenzaldehyde, 193, 666<br />
3-Dimethylaminobenzoic acid, 193<br />
4-Dimethylaminobenzoic acid, 193<br />
4-Dimethylaminobenzoin, 193<br />
4-Dimethylamino-1-butanol, 119<br />
2(Di-methylamino)ethanol, 104<br />
2-(Dimethylamino)ethyl methacrylate, 82, 83<br />
2-Dimethylaminoethyl urea, 105<br />
2-(Dimethylamino)-2-(hydroxymethyl)-1,3-propanediol, 253, 265<br />
5-Dimethylamino-3-methyl-1-pentanol, 99<br />
2-Dimethylamino-2-methyl-1-propanol, 253, 264, 265<br />
5-Dimethylaminonaphthalene-1-(2-aminoethyl)sulfonamide, 197<br />
4-Dimethylaminophenethanol, 666<br />
2-[4-(Dimethylamino)phenyl] ethanol, 669<br />
3-Dimethylamino-1,2-propanediol, 110<br />
1-(3-Dimethylaminopropoxy)-2-butanol, 104, 105<br />
N-(3-Dimethylaminopropyl)-2-ethylhexanoic acid amide, 99<br />
4-Dimethylaminopyridine, 199<br />
Dimethyl ammonium methyl sulfate, 695<br />
N,N-Dimethylaniline, 39, 192<br />
N,N-Dimethylbenzylamine, 99, 180<br />
2,5-Dimethyl-2,5-bis(benzoylperoxy)hexane, 182<br />
N,N-Dimethylcyclohexylamine, 99<br />
2,6-Dimethyl-3,5-diacetyl-1,4-dihydropyridine, 284<br />
2,5-Dimethyl-2,5-di(benzoylperoxy)hexane, 592<br />
2,5-Dimethyl-2,5-di(tert-butylperoxy)hexane, 516, 546, 591, 592, 594, 607, 621<br />
2,5-Dimethyl-2,5-di-tert-butylperoxyhexane, 595<br />
2,4-Dimethyl-2,5-di(tert-butylperoxy)-3-hexyne, 573<br />
2,5-Dimethyl-2,5-di(tert-butylperoxy)-3-hexyne, 516, 557, 592, 595, 597<br />
Dimethyldichlorosilane, 327<br />
Dimethyldiethoxysilane, 325<br />
2,5-Dimethyl-2,5-di(2-ethylhexanoylperoxy)hexane, 592<br />
2,5-Dimethyl-2,5-di(hydroperoxy)hexane, 591<br />
N,N-Dimethyl-N ′ ,N ′ -di(2-hydroxypropyl)-1,3-propane diamine, 483<br />
Dimethyldimethoxysilane, 325, 331<br />
2,3-Dimethyl-2,3-diphenylbutane, 627<br />
N,N-Dimethylethanolamine, 99, 100<br />
N,N-Dimethylethylamine, 99<br />
N,N-Dimethylethylethanolamine, 119<br />
N,N-Dimethylformamide, 544, 623<br />
2,5-Dimethylhexene-2,5-diperoxyisononanoate, 596
Index 737<br />
1,1-Dimethyl-3-hydroxybutyl-3-(carboxy)-5-norbornene-2-ylperoxycarboxylate,<br />
624<br />
1,1-Dimethyl-3-hydroxybutyl-2-(carboxy)perbenzoate, 624, 626<br />
1,1-Dimethyl-3-hydroxybutyl-2-(carboxy)peroxycyclohexanecarboxylate, 624<br />
1,1-Dimethyl-3-hydroxybutyl hydroperoxide, 626<br />
1,1-Dimethyl-3-hydroxybutyl-6-(hydroxy)peroxyhexanoate, 624<br />
1,1-Dimethyl-3-hydroxypropyl-3-(carboxy)peroxypropanoate, 624<br />
1,2-Dimethylimidazole, 101<br />
Dimethyl itaconate, 630<br />
Dimethylmelamine, 300<br />
Dimethylol butanoic acid, 93, 121<br />
α,α ′ -Dimethylol propionic acid, 124<br />
Dimethylol propionic acid, 120<br />
4,5-Dimethyl-2-oxo-1,3,2-dioxathiolane, 482<br />
N,N-Dimethyl-p-phenylene diamine, 6<br />
N ′ ,N ′ -Dimethylpiperazine, 99<br />
3,5-Dimethylpyrazole, 80<br />
Dimethyl sebacate, 476<br />
Dimethyl terephthalate, 35, 697<br />
3,5-Dimethylthio-toluene diamine, 93<br />
N,N-Dimethyl-p-toluidine, 479, 669, 672<br />
2,4-Dinitrotoluene, 74<br />
Dinonylphenol cyanate, 374<br />
Dioctyl adipate, 476<br />
Dioctyl glutarate, 476<br />
Dioctyl phthalate, 476<br />
7,26-Dioxatrispirobicyclo[4.1.0]heptane-4,5 ′ -1,3-dioxane-2 ′ ,2 ′′ -<br />
1,3-dioxane-5 ′′ ,4 ′′ -bicyclo[4.1.0]heptane, 665, 667<br />
3,23-Dioxatrispirotricyclo[3.2.1.0[2.4]]octane-6,5 ′ -1,3-dioxane- 2 ′ 2 ′′ -<br />
1,3-dioxane-5 ′′ ,7 ′′′ -tricyclo[3.2.1.0[2.4]octane], 185<br />
5-(2,5-Dioxotetrahydrofuryl)-3-methyl-3-cyclohexene-1,2-dicarboxylic<br />
anhydride, 180<br />
Dipentaerythritol pentaacrylate monophosphate, 684<br />
Dipentaerythritol pentamethacrylate monophosphate, 684<br />
Diphenylchlorosilane, 325<br />
Diphenyldimethoxysilane, 325<br />
N,N ′ -Diphenylethane-1,2-diamine, 6<br />
N,N-4,4-Diphenyl ether bismaleimide, 398<br />
o,o-Di-1-phenylethyl phenylphosphonate, 186<br />
N,N ′ -Diphenylhexane-1,6-diamine, 6<br />
Diphenyliodoniumhexafluorantimonate, 666<br />
Diphenyl iodonium hexafluoroantimonate, 192<br />
Diphenylmelamine, 300
738 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
N,N-4,4-Diphenylmethanebismaleimide, 398, 412<br />
4,4 ′ -Diphenylmethane bismaleimide, 547<br />
4,4 ′ -Diphenylmethane carbodiimide, 547<br />
4 ′ ,4 ′ -Diphenylmethane diamine, 87<br />
Diphenylmethane-4,4 ′ -diisocyanate, 69<br />
4,4 ′ -Diphenylmethanedimaleimide, 410<br />
Diphenylphosphine, 334<br />
3,3 ′ ,4,4 ′ -Diphenylsulfone tetracarboxylic dianhydride, 342<br />
1,3-Diphenyltetramethyldisilazane, 338<br />
Dipropylene glycol, 44<br />
2,2 ′ -Dipyridyl disulfide, 479<br />
2,3,8,9-Di(tetramethylene)-1,5,7,11-tetraoxaspiro[5.5]undecane, 141<br />
2,3,8,9-Di(tetramethylene)-1,5,7,11-tetraoxaspiro[5.5]undecane<br />
spiroorthocarbonate, 185<br />
2,14-Dithiacalix[4]arene, 248<br />
4,4 ′ -Dithiodianiline, 176<br />
6,6 ′ -Dithiodinicotinic acid, 479<br />
1,3-Divinyl-1,1,3,3-tetramethyldisiloxane, 333<br />
Dodecanoyl peroxide, 592, 597<br />
1-Dodecene, 147, 638<br />
2-Dodecen-1-yl succinic anhydride, 544<br />
Dodecenyl succinic anhydride, 180<br />
Dodecyl acrylate, 615<br />
Dodecyl aldehyde, 484<br />
Dodecyl diacid, 516<br />
Dodecyl mercaptane, 641<br />
Dodecylphenol, 381<br />
Eosine, 673<br />
Epichlorohydrin, 139–141, 148, 150, 173<br />
Epoxy allyl soyate, 141<br />
Epoxychlorotriazine, 565<br />
2-(3,4-Epoxycyclohexyl)ethyl(methyl)dimethoxysilane, 326<br />
2-(3,4-Epoxycyclohexyl)ethyl(phenyl)diethoxysilane, 326<br />
2-(3,4-Epoxycyclohexyl)ethyltriethoxysilane, 326<br />
2-(3,4-Epoxycyclohexyl)ethyltrimethoxysilane, 326<br />
3,4-Epoxycyclohexyl-methyl-3,4-epoxycyclohexane carboxylate, 141<br />
3,4-Epoxycyclohexylmethyl-3 ′ ,4 ′ -epoxycyclohexane carboxylate, 187<br />
Epoxy methyl soyate, 141<br />
E-12,13-Epoxyoctadeca-E-9-enoic acid ester, 141<br />
1,2-Epoxy-3-phenoxypropane, 159, 167<br />
2,3-Epoxypropoxy methacrylate, 663<br />
2,3-Epoxypropyl(methyl)dimethoxysilane, 326<br />
2,3-Epoxypropyl(phenyl)dimethoxysilane, 326
2,3-Epoxypropyltriethoxysilane, 326<br />
2,3-Epoxypropyltrimethoxysilane, 326<br />
2,3-Epoxypropyltrimethylammonium chloride, 523<br />
exo-3,6-Epoxy-1,2,3,6-tetrahydrophthalic anhydride, 142<br />
exo-3,6-Epoxy-1,2,3,6-tetrahydrophthalimidocaproic acid, 142<br />
17-β-Estradiol, 366<br />
Ethanolamine, 289, 561<br />
2-Ethenylisopropanol, 333<br />
Ethenylphenyloxirane, 141<br />
2-Ethoxyethyl cyanoacrylate, 473<br />
Ethyl acrylate, 91, 213, 214, 290, 351<br />
Ethylal, 286<br />
Ethylaluminum dichloride, 451<br />
Ethylamine, 289, 315<br />
Ethyl-(4,4 ′ -bismaleimidophenyl)phosphonate, 402, 422<br />
Ethyl α-(bromomethyl)acrylate, 189<br />
Ethyl cyanoacetate, 471<br />
Ethyl 2-cyanoacrylate, 472<br />
Ethyl cyanoacrylate, 473, 489<br />
Ethyl-3,3-di(tert-amylperoxy)butyrate, 596<br />
Ethyl diazoacetate, 631<br />
Ethyl-3,3-di(tert-butylperoxy)butyrate, 596<br />
N-Ethyldiisopropanolamine, 675<br />
Ethyl-4-dimethylamino benzoate, 193, 662, 666, 669, 673, 675<br />
N,N ′ -Ethylene-bisstearamide, 513<br />
Ethylene carbonate, 84<br />
Ethylene diamine, 86, 88, 93, 121, 454<br />
3,4-Ethylenedioxythiophene, 697<br />
Ethylene glycol, 3, 11, 89, 93, 117, 363, 369, 407, 495, 517, 697<br />
Ethylene glycol antimonite, 34<br />
Ethylene glycol dimethacrylate, 351, 662<br />
Ethylene oxide, 6, 85, 88, 173, 353, 566, 571<br />
Ethylene propylene diene monomer, 606<br />
Ethylene/propylene rubber, 557, 606<br />
Ethyl formate, 264<br />
2-Ethylhexyl acrylate, 151, 349, 351, 642<br />
2-Ethylhexyl alcohol, 352<br />
2-Ethylhexyl N-methacryloylcarbamate, 351, 352<br />
Ethyl hydroxymethyl oxazoline, 557<br />
Ethylmelamine, 300<br />
Ethyl methacrylate, 351, 365, 366<br />
Ethyl N-methacryloylcarbamate, 352<br />
2-Ethyl-4-methylimidazole, 176<br />
Index 739
740 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Ethylmethylphosphinic anhydride, 379<br />
N-Ethylmorpholine, 99–101<br />
Ethyltriethoxysilane, 325<br />
Ethyltrimethoxysilane, 325<br />
Ethynyl cyclohexanol, 334<br />
Ferric acetylacetonate, 107, 182<br />
9-Fluorenyl tetramethylene sulfonium hexafluoroantimonate, 187<br />
Fluorohectorite, 163<br />
Formaldehyde, 243, 245, 248, 310, 400, 416, 471<br />
Formic acid, 95, 304<br />
Fumaric acid, 3, 699<br />
Furan, 308, 407<br />
2,5-Fur<strong>and</strong>icarboxylic acid, 308<br />
2-Furan formaldehyde, 308<br />
Furfural, 243, 308<br />
Furfuraldehyde, 308<br />
Furfuryl alcohol, 308–310, 407<br />
2-Furfurylmethacrylate, 308<br />
Glutamic acid, 147<br />
Glutaric acid, 44, 90<br />
Glutaric anhydride, 180, 205, 626<br />
Glycerol, 3, 86, 89, 93, 363, 412, 522, 523, 559, 638<br />
Glycerol diglycidyl ether, 141<br />
Glycerol dimethacrylate, 688<br />
Glycerophosphate dimethacrylate, 684<br />
Glycerophosphoric acid, 684<br />
Glyceryl dimethacrylate phosphate, 684<br />
Glyceryl-2-phosphate, 684<br />
Glyceryl triacetate, 476<br />
Glyceryl tributyrate, 476<br />
3-Glycidoxypropyl(methyl)dibutoxysilane, 326<br />
3-Glycidoxypropyl(methyl)diethoxysilane, 326<br />
3-Glycidoxypropyl(methyl)dimethoxysilane, 326<br />
3-Glycidoxypropyltributoxysilane, 326<br />
3-Glycidoxypropyltriethoxysilane, 326<br />
(3-Glycidoxypropyl)trimethoxysilane, 210<br />
3-Glycidoxypropyltrimethoxysilane, 205, 326, 391<br />
Glycidyl acrylate, 12, 369<br />
Glycidyl methacrylate, 12, 141, 213, 536, 537, 554, 616, 635, 648, 660, 661<br />
Glycidyl phenyl ether, 186<br />
Glycol trilinoleate, 638<br />
Glyoxal, 243, 286<br />
Guttapercha, 449
Hectorite, 18<br />
3,3,4,4,5,5,5-Heptafluoro-1-pentene, 345<br />
Heptamethyltrisiloxane, 328<br />
Heptanoic anhydride, 639<br />
2-Heptanone, 268<br />
HET acid, 3, 5, 32–34<br />
HET anhydride, 180<br />
Hexa(allylamino)cyclotriphosphonitrile, 548<br />
Hexabromocyclododecane, 627<br />
2,2,3,3,4,4,5,5,6,6,7,7,8,8,9,9-Hexadecafluoro-decane-1,10-diol, 150<br />
2,4-Hexadienedioic acid, 573<br />
1,5-Hexadiyne, 493<br />
Hexafluoroisobutene, 148<br />
Hexafluoropropene, 366<br />
4,4 ′ -Hexafluoropropylidenebisphthalic dianhydride, 342<br />
Hexafunctional methacrylate ester, 660<br />
Hexahydro-4-methylphthalic anhydride, 180<br />
Hexahydrophthalic acid, 142<br />
Hexahydrophthalic anhydride, 163, 180<br />
Hexakis(methoxymethyl)melamine, 164<br />
Hexakis(methylol)melamine, 263<br />
Hexa(methoxymethyl)melamine, 263<br />
1,1,4,4,7,7-Hexamethylcyclo-4,7-diperoxynonane, 592<br />
Hexamethyldisilazane, 338<br />
Hexamethyldisiloxane, 331<br />
1,6-Hexamethylene-bis(2-furanylmethylcarbamate), 412<br />
N,N ′ -Hexamethylenebismaleimide, 410<br />
Hexamethylene diamine, 175, 177, 289<br />
1,6-Hexamethylenediisocyanate, 659<br />
Hexamethylene diisocyanate, 73, 119, 407<br />
Hexamethylenetetramine, 262–264<br />
Hexamethylol melamine, 300, 302<br />
Hexamethylphosphoramide, 623<br />
3,3,6,6,9,9-Hexamethylcyclo-1,2,4,5-tetraoxanonane, 592<br />
1,6-Hexane bismaleimide, 398<br />
1,6-Hexane diamine, 84<br />
Hexane-1,6-diamine, 69<br />
Hexane-1,6-diisocyanate, 69<br />
Hexanediol diglycidyl ether, 150<br />
1,6-Hexanediol dimethacrylate, 660, 662<br />
n-Hexanol, 12<br />
1-Hexene, 643<br />
tert-Hexyl hydroperoxide, 671<br />
Index 741
742 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
n-Hexyl isocyanate, 82<br />
tert-Hexylperoxybenzoate, 36<br />
High density poly(ethylene), 542<br />
Hydrazine, 88, 93<br />
Hydrazine monohydrate, 121<br />
Hydroquinone, 16, 17, 22, 481, 498, 555<br />
Hydroquinone monomethyl ether, 672, 677<br />
4-Hydroxyacetanilide, 159<br />
α-Hydroxy-acetophenone, 37<br />
3-Hydroxy-1-azabicyclo[2.2.2]octane, 99, 105<br />
Hydroxybenzoic acid, 498<br />
2-Hydroxybenzoquinone, 481<br />
2-[2-Hydroxy-3,5-bis(α,α-dimethylbenzyl)phenyl]-2H-benzotriazole, 356<br />
4-Hydroxybutyl acrylate, 91<br />
4-Hydroxybutylvinyl ether, 428<br />
3-Hydroxy-1,1-dimethylbutylperoxyneodecanoate, 596<br />
2-Hydroxy-4(2,3-epoxypropoxy)benzophenone, 142<br />
2-Hydroxyethyl acrylate, 27, 91<br />
2-Hydroxyethyl methacrylate, 123, 206, 351, 518, 558<br />
Hydroxyethyl methacrylate, 660<br />
Hydroxyethyl methacrylate monophosphate, 684<br />
(6-Hydroxy)hexyl-2-(trimethylaminonio)ethyl phosphate, 119<br />
2-Hydroxy-4-methoxybenzophenone, 356<br />
2-Hydroxy-4-methoxy-4 ′ -chlorobenzophenone, 356<br />
2-Hydroxymethyl-4,6-dimethylphenol, 260<br />
5-Hydroxymethylfurfural, 308, 309<br />
2-Hydroxy-2-methyl-1-phenyl-1-propane, 485<br />
2-Hydroxy-2-methylphenylpropane-1-one, 11, 37<br />
2-Hydroxy-2-methyl-1-phenyl-propan-1-one, 37, 38<br />
Hydroxy-2-methyl-1-phenyl-propanone, 193<br />
3-Hydroxymethyl quinuclidine, 105<br />
Hydroxynaphthoic acid, 498<br />
2-Hydroxy-4-octoxybenzophenone, 356, 683<br />
2-(2 ′ -Hydroxy-5 ′ -tert-octylphenyl)benzotriazole, 356<br />
N-(4-Hydroxyphenyl)maleimide, 402, 414, 416<br />
N-(p-Hydroxy)phenylmaleimide, 389<br />
2-Hydroxypropyl acrylate, 20, 210, 642<br />
1-(2-Hydroxypropyl)imidazole, 99<br />
p-Hydroxystyrene, 151<br />
6-Hydroxy-5-[(4-sulfophenyl)azo]-2-naphthalenesulfonic acid, 481<br />
(4-(2-Hydroxytetradecyloxyphenyl))phenyliodoniumhexafluoroantimonate, 192<br />
4-Hydroxy-2,2,6,6-tetramethyl-piperidin-1-oxyl, 615<br />
4-Hydroxy-2,2,6,6-tetramethyl-1-piperidinyloxy, 602
1-(3 ′ -(Imidazolinyl)propyl)urea, 99<br />
4-(3-Iodopropyl)benzocyclobutene, 643<br />
Isobutenylsuccinic anhydride, 672<br />
Isobutyl cyanoacrylate, 473<br />
Isobutyl vinyl ether, 190<br />
2-Isocyanatoethyl methacrylate, 351, 363, 660, 661<br />
Isophorone diamine, 93, 175<br />
Isophorone diisocyanate, 73, 76, 110, 118, 120, 121, 124<br />
Isophthalic acid, 3, 5, 35, 45, 89, 154, 697<br />
Isophthaloyl bis-4-benzocyclobutene, 493, 496<br />
Isophthaloyl dichloride, 516<br />
3-Isopropenyl-α,α-dimethylbenzene isocyanate, 546<br />
2-Isopropenyl-2-oxazoline, 573, 630<br />
1-(Isopropenylphenyl)-1,1-dimethylmethyl isocyanate, 82, 83<br />
Isopropoxybenzoin, 673<br />
Isopropyl alcohol, 167, 369<br />
Isopropyl chloride, 324<br />
Isopropyl myristate, 476<br />
Isosebacic acid, 44<br />
Itaconic acid, 3, 27, 620, 629<br />
Itaconic anhydride, 672<br />
3-Ketocoumarin, 209<br />
Lauric acid, 476<br />
Laurolactam, 572<br />
Lauroyl peroxide, 359, 362, 592<br />
Lauryllactam, 513<br />
Lead naphthenate, 107<br />
Lead octoate, 107<br />
Limonene, 142, 448, 449<br />
Linear low density poly(ethylene), 542, 635<br />
Linoleic acid, 638<br />
Lithium stearate, 515<br />
Longifolene, 449<br />
Low density poly(ethylene), 542, 620<br />
Lupeol, 449<br />
Lysine-diisocyanate, 73, 120<br />
Magnesium hydroxide, 539<br />
Magnesium oxide, 564<br />
Maleated poly(propylene), 541<br />
Maleic anhydride, 3, 15, 35, 113, 494, 541, 612, 616, 637<br />
p-Maleimidobenzoic anhydride, 424<br />
4-(N-Maleimidophenyl)glycidyl ether, 398, 402, 404<br />
4-Maleimidophenyl isocyanate, 407<br />
Index 743
744 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Manganese(III)acetylacetonate, 483<br />
Manganese octoate, 38<br />
Melam, 299<br />
Melamine cyanurate, 32, 111–113<br />
Melamine phosphate, 169, 526<br />
Melem, 299<br />
Melon, 299<br />
Menthane diamine, 175, 177<br />
2-Mercaptoethanol, 82, 641<br />
3-Mercapto-1,2-propanediol, 108<br />
Mercaptopropyltrimethoxysilane, 343<br />
Methacrylamide, 369<br />
2-Methacrylamide-2-methylpropenesulfonic acid, 571<br />
Methacrylate-terminated phosphoric acid ester, 684<br />
Methacrylic acid, 11<br />
Methacrylic anhydride, 84<br />
Methacryloxyethyl phosphate, 684<br />
4-Methacryloxyethyl trimellitate, 684<br />
3-Methacryloxypropoxytrimethoxysilane, 681<br />
(3-Methacryloxypropyl)trimethoxysilane, 23, 24<br />
3-Methacryloxypropyl-trimethoxysilane, 351, 365<br />
Methacryloyl-β-alanine, 660, 663<br />
Methacryloyl chloride, 82, 87<br />
Methacryloyl glutamic acid, 660<br />
Methacryloyl isocyanate, 351, 352<br />
Methacryloyloxyethane-1,1-diphosphonic acid, 684<br />
2-Methacryloyloxyethyldihydrogen phosphate, 671<br />
2-Methacryloyloxyethyl isocyanate, 351<br />
2-(Methacryloyloxy)ethyl phosphate, 665<br />
11-Methacryloyloxy-1,1-undecanedicarboxylic acid, 671<br />
2-Methoxybenzyl-1,3-propanediol, 184<br />
2-Methoxyethyl cyanoacrylate, 473<br />
Methoxyethylmorpholine, 103<br />
2-Methoxy-1-methylethyl cyanoacrylate, 473<br />
m-Methoxyphenol, 243<br />
p-Methoxyphenol, 481<br />
1-(2-Methoxyphenyl)piperazine, 116<br />
1-Methoxypoly(oxyethylene)benzocyclobutene, 493, 495<br />
Methoxypropyl cyanoacrylate, 488, 489<br />
4-Methoxy-2,2,6,6-tetramethyl-1-piperidinyloxy, 602<br />
Methyl acrylate, 8, 349, 351, 365, 637, 639<br />
Methylal, 286<br />
Methylamine, 289
Index 745<br />
9-Methylanthracene, 385<br />
2-Methyl-2,4-bis(2,3-epoxycyclohexyloxy)pentane, 202<br />
Methylbutynol, 334<br />
p-Methylcalix[6]arene, 189<br />
Methyl cyanoacrylate, 473<br />
4-Methylcyclohexylmethyl methacrylate, 350, 351<br />
Methyldichlorosilane, 327<br />
N-Methyldiethanolamine, 675<br />
Methyldiethanolamine, 359<br />
2-Methyl-2,5-dioxo-1-oxa-2-phospholane, 32, 33<br />
3-Methyl-1-dodecyn-3-ol, 334<br />
4,4 ′ -Methylene bis(2-chloroaniline), 93<br />
4,4 ′ -Methylene bis(3-chloro-2,6-diethylaniline), 93, 158<br />
4,4 ′ -Methylene bis[3-chloro-2,6-diethylaniline], 176<br />
4,4-Methylene biscyclohexyl diisocyanate, 73<br />
4,4 ′ -Methylene bis(cyclohexyl isocyanate), 111<br />
Methylene bis(4-phenyl isocyanate), 245<br />
α-Methylene-γ-butyrolactone, 660, 665<br />
4,4 ′ -Methylenedianiline, 158, 175, 402<br />
p,p ′ -Methylene diphenyl diisocyanate, 113<br />
4,4 ′ -Methylene diphenyl diisocyanate, 73<br />
1,1 ′ -(Methylene di-4,1-phenylene)bismaleimide, 416, 423<br />
N-(1-Methylethyl)-1-cyclohexyl-1-(diethylphosphono)nitroxide, 602<br />
2,2 ′ -[(1-Methylethylidene) bis[(2,6-dibromo-4,1-phenylene)oxy]]<br />
bis[4,6-bis[(2,4,6-tribromophenyl)oxy]]-1,3,5-triazine, 169<br />
1,1 ′ -(1-Methylethylidene)bis(4-(1-(2-furanylmethoxy)-<br />
2-propanolyloxy))benzene, 410<br />
2,2 ′ -[(1-Methylethylidene)bis(4,1-phenyleneoxymethylene)]bis(oxirane), 150<br />
Methylethylketone, 593<br />
Methylethylketone peroxide, 28, 36, 597<br />
Methylethylketoxime, 80<br />
(4-(1-Methylethyl)phenyl)(4-methylphenyl)iodonium tetrakis<br />
pentafluorophenylborate, 192<br />
2-Methylfuran, 313, 433<br />
5-Methylfurfural, 308<br />
5-[2-(5-Methyl furylene vinylene)]furancarboxyaldehyde, 317, 318<br />
3-Methyl-3-hydroxymethyl quinuclidine, 105<br />
2-(5-Methyl-2-hydroxyphenyl)benzotriazole, 356<br />
1-Methylimidazole, 101, 102, 176<br />
Methylisobutylketone, 593<br />
Methylisobutylketone peroxide, 593, 597<br />
Methylisopropylketone, 593<br />
Methyl-p-maleimidobenzoate, 424
746 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Methylmelamine, 300<br />
Methyl methacrylate, 8, 27, 351, 352, 354, 362, 365, 507, 634, 670<br />
Methyl N-methacryloylcarbamate, 351–353<br />
2-Methyl-1-[4-(methylthio)phenyl]-2-morpholinopropan-1-one, 193<br />
N-Methylmorpholine, 99, 101, 479<br />
Methyl nadic anhydride, 180<br />
7-Methyl-1,6-octadiene, 643<br />
2-Methylolphenol, 267<br />
4-Methylolphenol, 267<br />
2-Methylphenol, 259<br />
4-Methylphenol, 259<br />
Methylphenylchlorosilane, 325<br />
Methylphenyldichlorosilane, 328<br />
Methylphenyldiethoxysilane, 325<br />
Methylphenyldimethoxysilane, 325<br />
1-Methylpiperazine, 104<br />
2-Methyl-2-(4-piperidyl)-1,3-propanediol, 105<br />
2-Methyl-1,3-propanediol, 6, 14<br />
1-Methyl-3-propyl-5-butylmelamine, 300<br />
2-Methyl-1,3-propylene diol, 93<br />
Methylpropylketone peroxide, 40<br />
2-Methyl-2-(4-pyridyl)-1,3-propanediol, 105<br />
N-Methyl-2-pyrrolidone, 412, 421<br />
Methyl salicylate, 515<br />
α-Methylstyrene, 8, 328, 358<br />
3-Methyl-1,2,3,6-tetrahydrophthalic anhydride, 180<br />
Methyltetrahydrophthalic anhydride, 163, 180<br />
Methyltricaprylylammonium chloride, 148<br />
Methyltrichlorosilane, 327<br />
Methyltriethoxysilane, 325<br />
Methyltrimethoxysilane, 325, 331<br />
Methyltris(methylethylketoxime)silane, 331<br />
Methylvinyldimethoxysilane, 325<br />
Mica, 19, 109<br />
Monomethyl itaconate, 630<br />
Montmorillonite, 20<br />
cis,cis-Muconic acid, 573<br />
cis,trans-Muconic acid, 573<br />
Myrcene, 449, 465<br />
Myristic acid, 366<br />
Nadic anhydride, 400, 401, 637<br />
1,5-Naphthalene diamine, 175, 178<br />
1,5-Naphthalene diisocyanate, 73
Index 747<br />
Naphthalene-1,5-diisocyanate, 69<br />
β-Naphthol, 243<br />
2-Naphthol, 419<br />
1,2-Naphthoquinonediazide, 268<br />
Naphthoquinonediazidesulfonic acid, 268<br />
1-(α-Naphthyl)-3,3-di(2-hydroxyethyl)-triazene-1, 93<br />
Natural rubber, 456, 461, 568<br />
Neopentyl(diallyl)oxy tri(dioctyl)pyrophosphatotitanate, 25<br />
Neopentyl glycol, 3, 5, 44, 90, 245, 362<br />
Nitrokonjac glucomannan, 117<br />
3-Nitroperoxybenzoic acid, 148<br />
4-Nitroperoxybenzoic acid, 148<br />
4,4 ′ -Nitrophenylazoaniline, 210<br />
o-Nitrotoluene, 74<br />
p-Nitrotoluene, 73<br />
Nonafluorohexene, 345<br />
Nonylphenol, 381<br />
Norbornane diketimine, 176<br />
5-Norbornene-2,3-dicarboxylic anhydride, 400<br />
1-Octadecanethiol, 514<br />
2,2,3,3,4,4,5,5-Octafluoro-hexane-1,6-diol, 150<br />
Octamethylcyclotetraoxysilane, 540<br />
1-Octene, 147<br />
2-Octen-1-ylsuccinic anhydride, 671<br />
n-Octylamine, 483<br />
2-Octyl cyanoacrylate, 473<br />
Octyl mercaptane, 641<br />
(4-Octyloxyphenyl)phenyliodonium hexafluoroantimonate, 192<br />
p-Octylphenyl salicylate, 356<br />
Oxalic acid, 242<br />
2-(6-Oxid-6H-dibenz[c,e][1,2]oxa-phoshorin-6-yl)-1,4-benzenediol, 141<br />
2-(6-Oxid-6H-dibenz[c,e][1,2]oxa-phosphorin-6-yl)-1,4-benzenediol, 168<br />
2-(6-Oxid-6H-dibenz[c,e][1,2]oxaphosphorin-6-yl)methanol, 168<br />
4-Oxo-2,2,6,6-tetramethyl-1-piperidinyloxy, 602<br />
2,2 ′ -Oxybis(N,N-dimethylethanamine), 103<br />
4,4 ′ -Oxydianiline, 407<br />
3,3 ′ -(Oxydi-p-phenylene)bis(2,4,5-triphenylcyclopentadienone), 410<br />
4,4 ′ -Oxydiphthalic anhydride, 498<br />
Palmitic anhydride, 639<br />
Paraformaldehyde, 243, 245, 257, 262, 472<br />
Pentabromobenzyl acrylate, 501<br />
Pentaerythritol, 86, 90, 245, 291, 526, 622<br />
Pentaerythritol triacrylate, 516
748 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Pentaerythritol triacrylate monophosphate, 684<br />
Pentaerythritol trimethacrylate monophosphate, 665, 684<br />
1,2,3,4,5-Pentamethylcyclopenta-1,3-dienide, 428<br />
N,N,N ′ ,N ′ ,N ′′ -Pentamethyldiethylene triamine, 99<br />
3,6,6,9,9-Pentamethyl-3-(ethyl acetate)1,2,4,5-tetraoxacyclononane, 592<br />
3,6,6,9,9-Pentamethyl-3-n-propyl-1,2,4,5-tetraoxacyclononane, 592<br />
2,4-Pent<strong>and</strong>ione, 27<br />
Perfluoro (alkyl vinyl ether), 467<br />
Peroxyacetic acid, 147<br />
Perylene(peri-dinaphthalene), 384<br />
Phell<strong>and</strong>rene, 449<br />
Phenol, 243, 259, 295, 307, 344, 452, 640<br />
Phenolphthalein, 412<br />
Phenolphthalein poly(ether ether ketone), 155<br />
N-(1-Phenylbenzyl)-((1-diethylphosphono)-1-methyl ethyl)nitroxide, 602<br />
Phenyl-(4,4 ′ -bismaleimidophenyl)phosphonate, 402, 422<br />
3-Phenyl-3-tert-butylperoxyphthalide, 592<br />
p-Phenyl diamine, 400<br />
N-Phenyldiethanolamine, 699<br />
N-Phenyl-1-diethylphosphono-2,2-dimethylpropyl nitroxide, 602<br />
N-Phenyl-1-diethylphosphono-1-methyl ethyl nitroxide, 602<br />
1-Phenyl-3,3-di(2-hydroxyethyl)-triazene-1, 93<br />
1,3-Phenylene-bis(2-oxazoline), 514<br />
2,2 ′ -(1,3-Phenylene)bis(2-oxazoline), 564<br />
2,2 ′ -(1,4-Phenylene)bisoxazoline, 547<br />
3,3 ′ -(p-Phenylene)bis(2,4,5-triphenylcyclopentadienone), 410<br />
m-Phenylene diamine, 175, 178, 198, 272, 414<br />
N,N ′ -m-Phenylenedimaleimide, 410, 547<br />
N,N ′ -o-Phenylenedimaleimide, 410<br />
N,N ′ -p-Phenylenedimaleimide, 410<br />
4,4 ′ -[1,3-Phenylene(1-methyl ethylidene)]bisaniline, 498<br />
Phenyl glycidyl ether, 142, 194<br />
N-Phenylglycine, 193<br />
2-Phenyl-2-imidazoline, 483<br />
N-Phenylmaleimide, 182, 416, 428<br />
Phenylmelamine, 300<br />
Phenyl N-methacryloylcarbamate, 351–353<br />
N-(1-Phenyl-2-methylpropyl)-1-diethylphosphono-1-methyl ethyl nitroxide, 602<br />
o-Phenylphenol, 168<br />
Phenylphosphonic acid, 186<br />
3-Phenyl-1-propanol, 567<br />
Phenyltrimethoxysilane, 30, 325<br />
Phlogopite, 291
Index 749<br />
Phosgene, 70<br />
Phosphorus oxychloride, 186<br />
Phthalic anhydride, 3, 5, 14, 35, 44, 89, 103, 113, 154, 180, 556, 626, 697<br />
Phthaloyl chloride, 390<br />
Picric acid, 17<br />
Pimaric acid, 449<br />
Pimelic acid, 44<br />
Pinane hydroperoxide, 591<br />
α-Pinene, 449<br />
β-Pinene, 449<br />
Piperidine, 186<br />
Polyamide 6, 629<br />
Poly(benzo[1,2-d4,5-d ′ ]bisthiazole-2,6-diyl)-1,4-phenylene, 495<br />
Poly(butylene terephthalate), 214, 525, 541<br />
Poly(ε-caprolactam), 550<br />
Poly(ε-caprolactone), 480, 517, 518, 522, 523, 525<br />
Poly(carbonate)dimethacrylate, 660<br />
Poly(2,6-dichloro-1,4-phenylene oxide), 555<br />
Poly(2,6-dimethyl-1,4-phenylene ether), 565<br />
Poly(2,6-dimethyl-1,4-phenylene oxide), 549, 555<br />
Polydioxanone, 488<br />
Poly(2,2-di(4-phenylene)propane phthalate), 390<br />
Poly(2,2-di(4-phenylene)propane phthalate-co-2,2-di(4-phenylene)propane<br />
isophthalate), 390<br />
Poly(2,2-di(4-phenylene)propane phthalate-co-2,2-di(4-phenylene)propane<br />
terephthalate), 390<br />
Poly(epichlorohydrin), 111, 112<br />
Poly(ether ether ketone), 154<br />
Polyetherimide, 417<br />
Poly(ethylene-co-glycidyl methacrylate), 552<br />
Poly(ethylene glycol)dimethacrylate, 351, 363, 662<br />
Poly(ethylene glycol)methacrylate, 518<br />
Poly(ethylene 2,6-naphthalate), 555<br />
Poly(ethylene-octene) copolymer, 551<br />
Poly(ethylene oxide), 153, 206, 533<br />
Poly(ethylene terephthalate), 342<br />
Poly(glycolic acid), 480<br />
Polyglycolic acid, 488<br />
Poly(p-hydroxybenzoate), 555<br />
Poly(β-hydroxybutyrate-co-β-hydroxyvalerate), 517<br />
Poly(3-hydroxybutyric acid), 480<br />
Polyhydroxy fullerene, 144<br />
3,4-Poly(isoprene), 459
750 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Poly(lactic acid), 480<br />
Polylactic acid, 488, 519<br />
Poly(lactide), 521<br />
Poly(methyl methacrylate), 153, 533<br />
Poly(oxypropylene)diamine, 205<br />
Polyoxypropylene glycol, 389, 390<br />
Poly(p-phenylene benzobisthiazole), 498<br />
Poly(phenylene ether), 214<br />
Poly(phenylene sulfide), 559<br />
Poly(phthaloyl diphenyl ether), 418<br />
Poly(phthaloyl diphenyl ether-co-isophthaloyl diphenyl ether), 418<br />
Poly(propylene), 607<br />
Poly(propylene oxide)diamine, 176<br />
Poly(styrene), 152, 557<br />
Poly(styrene-co-acrylonitrile), 153<br />
Poly(styrene-b-(ethylene-co-butylene)), 542<br />
Polysulfone, 390<br />
Poly(tetramethylene ether), 513<br />
Polytetramethylene glycol, 119<br />
Poly(thiophene), 645<br />
Polyurethane dimethacrylate, 659, 660<br />
Poly(vinyl acetate), 26<br />
Poly(vinyl chloride), 98<br />
Poly(vinyl chloride-co-vinyl acetate), 26<br />
Poly(vinyl chloride-co-vinyl acetate-co-maleic anhydride), 26<br />
Poly(vinylidene difluoride-co-hexafluoropropylene), 435<br />
Poly(vinylidene fluoride), 561<br />
Potassium hydroxide, 16<br />
Pristine, 20<br />
1,2-Propanediol, 44<br />
Propanephosphonic anhydride, 379<br />
1,3-Propanesulfone, 119<br />
2-Propenylphenol, 418<br />
β-Propiolactone, 119<br />
Propionaldehyde, 243<br />
Propionamide, 263<br />
4-Propoxy-2,2,6,6-tetramethyl-piperidin-1-oxyl, 615<br />
Propylamine, 289<br />
N-Propyldiethanolamine, 675<br />
1,2-Propylene glycol, 3, 11, 14<br />
Propylene glycol, 89, 93, 363, 366, 697<br />
Propylene oxide, 6, 85, 86, 88, 545, 571<br />
1-Pyrenesulfonyl chloride, 196
Pyrogallol, 481<br />
2,2 ′ -Pyromellitdiimidodisuccinic anhydride, 92<br />
Pyromellitic dianhydride, 36, 166, 180, 524<br />
Pyrophosphoric acid, 489<br />
Quinacridone, 695<br />
o-Quinodimethane, 495<br />
3-Quinuclidinol, 105<br />
Rectorite, 109<br />
Resin-modified glass ionomer cements, 663<br />
Resorcinol, 243<br />
Resorcinol dicyanate, 377<br />
Retinol, 449<br />
Rice starch, 629<br />
Ricinoloxazoline maleate, 634<br />
Rosin, 450<br />
Rutile, 365<br />
Sago starch, 544<br />
Salicylaldehyde, 147<br />
Salicylic acid, 103<br />
Sebacic acid, 3, 45<br />
Silicon oxycarbide, 338<br />
Sisal, 25, 553<br />
Sodium ascorbate, 334<br />
Sodium dodecyl sulfate, 644<br />
Sodium dodecylsulfate, 697<br />
Sodium hypochlorite, 148<br />
Sodium stearate, 565<br />
Sodium sulfoisophthalate, 697<br />
Sorbitol, 522<br />
Sorbitol monoethoxylate, 522<br />
Soy flour, 121<br />
Squalene, 449<br />
Stannous octoate, 107, 525<br />
Starch, 121<br />
Strychnine, 344<br />
Styrene, 616<br />
Styrene butadiene rubber, 465<br />
Styrene-ethylene/butylene-styrene triblock copolymer, 541<br />
Styrene-b-(ethylene-co-1-butene)-b-styrene triblock copolymer, 542<br />
Styrene oxide, 141, 142<br />
p-Styrenesulfonic acid, 571, 647<br />
Succinic acid, 90<br />
Sucrose, 86, 205<br />
Index 751
752 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Sulfanilamide, 146, 176<br />
3-Sulfolene, 481<br />
5-Sulfonatoisophthalic acid, 11<br />
Sulfonic acid, 119, 324, 481, 644<br />
2-Sulfonyl(meth)acrylate, 571<br />
Sulfur dioxide, 472, 481, 482<br />
Tapioca starch, 545<br />
Tartaric acid, 120, 311<br />
Terephthalic acid, 3, 5, 11, 35, 45, 89, 498, 555, 697<br />
Terephthaloylbis(4-oxybenzoic) acid, 141<br />
Terephthaloyl dichloride, 498, 516<br />
Terpinene, 449<br />
α-Terpineol, 201<br />
Terpinolene, 449, 454<br />
2,6,2 ′ ,6 ′ -Tetrabromobisphenol A, 32<br />
Tetrabromobisphenol A, 3, 142, 168, 169, 357<br />
Tetrabromophthalic anhydride, 3, 32, 33<br />
α,α,α ′ ,α ′ -Tetrabromo-o-xylene, 493<br />
Tetra-n-butylammonium chloroacetate, 103<br />
Tetra-n-butylammonium cyanoborohydride, 484<br />
Tetra-n-butyl ammonium fluoride, 483<br />
Tetrabutylphosphonium acetate, 515<br />
Tetrabutyltitanate, 421<br />
Tetrachloromethane, 623<br />
Tetrachlorophthalic anhydride, 27<br />
1-Tetradecene, 147<br />
Tetraethoxysilane, 110, 167, 325, 345, 681<br />
3,3 ′ ,5,5 ′ -Tetraethyl-4,4 ′ -diaminodiphenylmethane, 175<br />
Tetraethylene glycol dimethacrylate, 662<br />
N,N,N ′ ,N ′ -Tetraethylethylene diamine, 483<br />
Tetrafluoroethylene, 467<br />
Tetraglycidyl diaminodiphenylmethane, 524<br />
Tetraglycidyl-4,4 ′ -diaminodiphenylmethane, 144, 153<br />
Tetrahydrofuran, 85, 309, 366, 414, 666<br />
Tetrahydrofurfuryl cyclohexene dimethacrylate, 660<br />
Tetrahydrofurfuryl methacrylate, 660, 661<br />
Tetrahydrophthalic anhydride, 11, 180, 697<br />
Tetrahydrophthalimide, 309<br />
Tetrakis(4-hydroxyphenyl)ethane, 142<br />
1,1,2,2-Tetramethoxyethane, 286<br />
Tetramethoxysilane, 30, 325<br />
Tetramethylammonium pivalate, 106<br />
N,N,N ′ ,N ′ -Tetramethyl-1,3-butane diamine, 483
Index 753<br />
Tetramethyldivinyldisiloxane, 331<br />
N,N,N ′ ,N ′ -Tetramethylethylene diamine, 483<br />
2,2,6,6-Tetramethyl-4-hydroxypiperidine-1-oxyl monophosphonate, 602<br />
2,2,6,6-Tetramethyl-1-piperidinyloxy, 602, 603, 643<br />
Tetramethyl-1-piperidinyloxy, 568<br />
2,2,5,5-Tetramethyl-1-pyrrolidinyloxy, 602, 603<br />
m-Tetramethylxylene diisocyanate, 75, 76<br />
Tetrapropoxysilane, 325<br />
Thermoplastic starch, 559<br />
2,2 ′ -Thiobis[4-tert-butylphenol], 248<br />
Thiourea, 299<br />
Thiuram disulfide, 608<br />
Tin-di-n-butyl-di-3,5-amino benzoate, 109<br />
Tin oxide, 357<br />
Titanium n-butoxide, 200<br />
Titanocene, 673<br />
Toluene diamine, 86<br />
2,4-Toluene diisocyanate, 73, 123<br />
2,6-Toluene diisocyanate, 73<br />
Toluene diisocyanate, 407<br />
p-Toluenesulfonic acid, 15, 79, 242, 311, 312, 324, 400<br />
Tosyl isocyanate, 108<br />
Triallyl cyanurate, 8, 10<br />
Triallyl isocyanurate, 211, 548<br />
2,5,8-Triamino-1,3,4,6,7,9,9b-heptaazaphenalene, 299<br />
Triarylsulfonium hexafluoroantimonate, 208<br />
1,5,7-Triazabicyclo[4.4.0]dec-5-ene, 483<br />
1,3,5-Triazine-2,4,6-triamine, 299<br />
Tributylamine, 675<br />
Tri-n-butylborane, 668<br />
Tributylborane, 672<br />
Tributylphosphine, 483<br />
1,2,4-Trichlorobenzene, 567<br />
Tri(p-chloro phenyl)phosphine, 253<br />
Tri(p-cresyl)phosphate, 476<br />
Tricresyl phosphate, 357<br />
Triethanolamine, 86, 104, 208, 284, 293, 669, 675<br />
Triethylamine, 99, 101, 121, 253, 264, 265, 514, 544<br />
Triethylborane, 670<br />
Triethyl citrate, 366<br />
Triethylene diamine, 101<br />
Triethylene glycol diacrylate, 369<br />
Triethylene glycol dimethacrylate, 659–661, 675
754 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Triethylene glycol divinyl ether, 10<br />
Triethylene glycol methylvinyl ether, 187<br />
Triethylenetetramine, 175<br />
Tri(2-ethylhexyl)phosphate, 476<br />
Triethyl phosphate, 111, 112, 476<br />
Triethyl phosphite, 623<br />
3,6,9-Triethyl-3,6,9-trimethyl-1,4,7-triperoxonane, 594, 607<br />
Triflic acid, 185, 322<br />
Trifluoromethanesulfonic acid, 185<br />
3,3,3-Trifluoropropyltrimethoxysilane, 325<br />
Triglycidyl isocyanurate, 141<br />
Triglycidyloxy phenyl silane, 141, 168, 169<br />
Triisopropanolamine, 675<br />
Trimellitic anhydride, 11<br />
Trimercaptothioethylamine, 176<br />
Trimercaptotriethylamine, 208<br />
1,2,4-Trimethoxybenzene, 193<br />
Trimethoxysilane, 391<br />
3-(Trimethoxysilyl)propyl methacrylate, 631<br />
Trimethylamine, 268<br />
2,4,6-Trimethylbenzoyldiphenylphosphine oxide, 37, 39, 662<br />
Trimethylborate, 311<br />
Trimethylchlorosilane, 327<br />
3,7,11-Trimethyl-1-dodecyn-3-ol, 334<br />
Trimethylene glycol-di-p-aminobenzoate, 93<br />
3,5,5-Trimethylhexanoyl peroxide, 592<br />
Trimethylmelamine, 300<br />
Trimethylolethane, 245<br />
1,1,1-Trimethylolpropane, 76, 89, 93<br />
Trimethylolpropane, 3, 86, 89, 245<br />
Trimethylolpropane diallyl ether, 11<br />
1,1,1-Trimethylolpropane dipropenyl ether, 10<br />
Trimethylolpropane mono allyl ether, 3<br />
1,1,1-Trimethylolpropane triacrylate, 473, 632<br />
Trimethylolpropane triacrylate, 351, 513, 638<br />
1,1,1-Trimethylolpropane trimethacrylate, 660<br />
Trimethylolpropane trimethacrylate, 27<br />
Trimethylolpropyl trimethacrylate, 662<br />
2,4,6-Trimethylphenol, 259<br />
4-Trimethylsiloxybenzocyclobutene, 493<br />
Trioctyl trimellitate, 476<br />
Trioxane, 243<br />
Triphenylphosphine, 253
Triphenylphosphine oxide, 428<br />
Triphenyl phosphite, 565<br />
2,4,6-Triphenylpyrylium tetrafluoroborate, 485<br />
Tripropylamine, 675<br />
Tripropylene glycol diacrylate, 638<br />
Tris(2-allylphenoxy)-s-triazine, 435<br />
Tris(2-allylphenoxy)triphenoxy cyclotriphosphazene, 435<br />
Tris(2-aminoethyl)amine, 484<br />
Tris(2-chloroethyl)phosphate, 357<br />
2,3-Tris(dibromopropylene)phosphate, 627<br />
2,4,6-Tris(dimethylaminomethyl)phenol, 106, 179<br />
1,3,5-Tris(3-dimethylaminopropyl)-s-hexahydrotriazine, 101<br />
N,N ′ ,N ′′ -Tris(5-hydroxy-3-oxapentyl)melamine, 300<br />
1,1,1-Tris(4-hydroxyphenyl)ethane, 210<br />
Tris(2-hydroxyphenyl)phosphine oxide, 169<br />
Trismercaptopropionate, 427<br />
Tris(p-toluenesulfonato)iron(III), 697<br />
2,4,6-Tris(2,4,6-tribromophenoxy)-1,3,5-triazine, 169<br />
Trypsin, 647<br />
Turpentine, 450<br />
10-Undecene-1-ol, 644<br />
10-Undecenyl sulfate, 644<br />
Urethane dimethacrylate, 675<br />
Vanadium acetylacetonate, 38<br />
Vermiculite, 273, 291<br />
Vernonia oil, 141<br />
Vinyl acetate, 290, 634<br />
Vinylbenzyldodecyldimethyl ammonium chloride, 20<br />
Vinylbenzyloctadecyldimethyl ammonium chloride, 20<br />
Vinyl-4-tert-butylbenzoate, 638<br />
N-Vinyl carbazole, 190<br />
4-Vinyl-1-cyclohexene, 328, 329<br />
Vinylcyclohexene epoxide, 141<br />
N-Vinylformamide, 285<br />
Vinylidene fluoride, 366<br />
Vinyloxazoline, 573<br />
Vinylpyridine, 8<br />
1-Vinyl-2-pyrrolidinone, 290<br />
N-Vinyl pyrrolidone, 641<br />
Vinylpyrrolidone, 52<br />
p-Vinyltoluene, 8<br />
Vinyltriethoxysilane, 631<br />
Vinyltriethylsilane, 631<br />
Index 755
756 <strong>Reactive</strong> <strong>Polymers</strong> <strong>Fundamentals</strong> <strong>and</strong> <strong>Applications</strong><br />
Vinyltrimethoxysilane, 325, 631<br />
Vinyltrimethylsilane, 631<br />
Wollastonite, 23, 24<br />
Zeolite, 109<br />
Zinc chloride, 311<br />
Zinc 2-ethylhexanoate, 360<br />
Zinc hexacyanocobaltate, 87<br />
Zinc hydroxystannate, 32<br />
Zinc naphthenate, 381<br />
Zinc octoate, 334, 381<br />
Zinc stearate, 25, 695<br />
Zirconium hydroxide, 357<br />
Zirconium oxide, 677, 678<br />
Zirconium tetrachloride, 179<br />
Zirconyl chloride, 681<br />
Zirconyl dimethacrylate, 681
757<br />
GENERAL INDEX<br />
Index Terms<br />
Links<br />
Ablative properties<br />
allyl boron compounds 419<br />
AC-calorimeters 194<br />
Acceleration<br />
gelation 168<br />
polymerization 42 477<br />
Accelerators 38<br />
crosslinking 331<br />
crown ethers 478<br />
cyanoacrylates 477<br />
dental polymers 669<br />
ester-type 264<br />
Acetals<br />
cosolvents for UF 286<br />
cyclic 91 658<br />
dichlorobenzaldehyde 206<br />
melamine/urea/formaldehyde resins 286<br />
Acetylation<br />
sisal 553<br />
starch 639<br />
Acid-base reactions 697<br />
Acidolysis reaction<br />
poly(carbonate) 561<br />
polyester 555<br />
Acoustic ceiling tiles 303<br />
Acrylic resins<br />
films 365<br />
Adhesion<br />
amino-functionalized polysiloxane 345<br />
coupling agent 391<br />
coupling sites 269<br />
cyanate ester resin 391<br />
dental polymer 682<br />
graphite/bismaleimide composite 435<br />
hybrid resins 160<br />
interfacial 523<br />
interlaminar 19<br />
plasma activation 648<br />
self-assembling polymers 343<br />
sisal fibers 553<br />
tackifiers 456<br />
terpene phenol resin 463<br />
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758<br />
Index Terms<br />
Links<br />
to glass fibers 8 23<br />
to Kevlar fiber 434<br />
to nonpolar substrates 483<br />
to oily surfaces 156<br />
Aerobic degradation 519<br />
Aerodams 517<br />
Aerospace applications 24 197 322<br />
Aerospaceapplications 373<br />
Agave sisalana 552<br />
Agricultural applications 245 295 308<br />
Alder-ene reaction 400 642 643<br />
Alkenoylcarbamates 352<br />
Allophanate 92<br />
Amalgam replacement 657<br />
Amphiphilic polymers 141<br />
Anti-punk properties 255<br />
Antibodies 433<br />
Anticarcinogenic activity 142<br />
Antifoaming agents 340<br />
Antifouling compositions 344<br />
Antioxidants 338<br />
chewing gum 466<br />
grafted 632<br />
Antiplasticizers 159<br />
hyperbranched polymers 144<br />
Antistatic formulations 167 360<br />
Aryl cyanates<br />
hydrolysis 375<br />
Autocatalysis<br />
isocyanate 114<br />
phenol 179<br />
Autocatalytic curing 379 382 427<br />
Autocatalytic polyol 88<br />
Automotive applications 98 160 203 241 322 517<br />
Backbiting 423 520<br />
Backcoats 343<br />
Bagasse 24 307<br />
Base-catalyzed<br />
equilibration polymerization 325<br />
inorganic bases 253<br />
Batch cell method 353<br />
Batteries 167 363<br />
lithium 122<br />
Benzene yellow 695<br />
Beverage containers 525<br />
Binders<br />
abrasive 266<br />
friction 266<br />
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759<br />
Index Terms<br />
Links<br />
glass fibers 251 266 294 316<br />
petroleum recovery 266<br />
s<strong>and</strong> 266 316<br />
Bioabsorbable polymers 488<br />
Biocomposites 363<br />
Biodegradability<br />
poly(lactide) 521<br />
starch 522<br />
Biodegradable<br />
composites 161<br />
compositions 517<br />
epoxy-polyester resins 205<br />
grafted polymer 518<br />
Lysine-diisocyanate 73<br />
poly(lactide) 521<br />
polyesters 52<br />
terpene resins 459<br />
Biofibers 161<br />
Biuret 92 96<br />
Blow molding 524<br />
Blowing<br />
chemical 94<br />
epoxy resins 203<br />
formic acid 95<br />
physical 95<br />
Blowmolding 517<br />
Bonding<br />
adhesive 648<br />
adhesives 475<br />
chemical 24 154 254<br />
covalent 648<br />
hydrogen 122 488 639<br />
interfacial 22 161 212<br />
interphase 152 535<br />
polyolefin substrates 485<br />
primers 482<br />
Bone cement 49 52 688<br />
Bookbindery 462<br />
Boron trifluoride complexes 175 179<br />
Bottles 46 519<br />
Bragg reflector mirrors 504<br />
Brake composites 273<br />
Bridges<br />
dental 672<br />
ether 286<br />
methylene 248 251 286 312<br />
methylene-ether 310<br />
phenoxy 261<br />
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760<br />
Index Terms<br />
Links<br />
silicon groups 402<br />
Brittleness 1 155 255 397 466 501<br />
519 700<br />
Brunauer Emmett Teller equation 543<br />
Bubbles 38 273 356 462<br />
Building materials 47 204 340 360 365 368<br />
Bumpers 517<br />
Cables 341 631<br />
Calcification 120<br />
Capacitors 164 363<br />
Capillary flow microreactor 304<br />
Carbon<br />
glass-like 271 313<br />
Carbon black 694<br />
Carbonylation<br />
propyne 353<br />
urethane 70<br />
Carboxybetaine<br />
grafting 119<br />
Carboxylation 272<br />
Caries 682<br />
Cashew nut shell liquid 25<br />
Cassava 544<br />
Cast elastomers 69<br />
Casting 47 116 182 204<br />
polymerization 358<br />
s<strong>and</strong> binders 313<br />
steel 294<br />
syrups 349<br />
Catalysis<br />
acidolysis 561<br />
copolyesterification 14<br />
enzymatic degradation 488<br />
isomerization 6<br />
latent 107<br />
titanium dioxide 428<br />
urethane 103<br />
zwitterions 103<br />
Catalysts<br />
addition-fragmentation 190<br />
delayed-action 103 179<br />
latent 107 176 184 311 386<br />
organometallic 106<br />
Cavitation<br />
shear b<strong>and</strong>ing 152<br />
ultrasonic curing 312<br />
Ceiling temperature 482 510 511 617 620<br />
Cement<br />
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761<br />
Index Terms<br />
Links<br />
bone 52<br />
dental 669<br />
furan resins 313<br />
Ceramics<br />
aluminum nitride 421<br />
microcellular 338<br />
synthesis by pyrolysis 336<br />
Chain<br />
branching 608<br />
entanglements 26 166<br />
reversible termination 567<br />
Chain extenders 110 121 156 400 514 524<br />
diols 31<br />
for polyesters 52<br />
glycols 92<br />
photosensitive 92<br />
waterborne 93<br />
Chain extension<br />
BCB 498<br />
Diels-Alder reaction 407<br />
diglycidyl compound 525<br />
Michael addition 407<br />
polyaddition 524<br />
Chain scission 534 590<br />
shear induced 614<br />
UV 365<br />
Chain stoppers 330 498<br />
undecanol 3<br />
Chain transfer 184 343 514 587 631<br />
mercaptan 82 641<br />
Charge carrier 51<br />
Charge control<br />
toner 51<br />
Charring<br />
agents 112<br />
aromatic polyesters 89<br />
Chelates 38 122 123 182<br />
Chemoreceptors 189<br />
Chewing gums 465<br />
Chitin<br />
N-deacetylation 118<br />
Chlorodioxins 292<br />
Chlorofluorocarbons<br />
blowing 95<br />
Chlorosulfonation 434<br />
Chromatography<br />
packing materials 314<br />
stationary phases 189<br />
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762<br />
Index Terms<br />
Links<br />
Chrome yellow 695<br />
Chromophore<br />
conjugated furans 317<br />
Disperse Orange 3 209<br />
maleimide 427<br />
phenylazo-benzothiazoles 210<br />
Clay, see also Oganoclays 162<br />
Hectorite 18<br />
macroporous 271<br />
nanocomposites 540<br />
organo 162<br />
organophilic 20<br />
Rectorite 109<br />
Cloud point 152 157 195 454 458<br />
Co-condensation<br />
melamine <strong>and</strong> urea 302<br />
urea resins 286<br />
Co-continuous phase 27 167 389 390 417 543<br />
Coagulation 304<br />
Coal-tar pitches 315<br />
Coalescence<br />
dispersed droplets 211<br />
dispersed phase 538 540<br />
prevention 546<br />
viscosity dependence 211<br />
Coatings 1 3 48 86 120 180<br />
203 322 365 422 463<br />
waterborne 203<br />
Coconut shells 270<br />
Coefficient<br />
diffusion 687<br />
extinction 192<br />
friction 50 199 465<br />
heat transfer 509<br />
thermal conductivity 509<br />
thermal expansion 146 375 400<br />
Cohesion 352 461 701<br />
Cohesion energy density 621<br />
Colloidal silica 688 695<br />
Colorant 51 466<br />
Colorants 694<br />
Coloration 15<br />
Coloring agents<br />
toners 694<br />
Comb-like polymers 82 87 484<br />
Combustion 30 116 292 336 666<br />
Comonomer assisted grafting 633<br />
Compatibilizers<br />
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763<br />
Index Terms<br />
Links<br />
block copolymers 157<br />
epoxy resins 212<br />
grafted polymers 615<br />
UP resin 49 53<br />
Composites 397<br />
hydrophobic 665<br />
rigid rod-like 498<br />
wood flour 541<br />
Condensation<br />
base-catalyzed 471<br />
Calixarenes 189<br />
crosslinking 334<br />
hydrolytic 322<br />
intermolecular 330<br />
Knoevenagel 472<br />
resols 247<br />
Conducting glues 167<br />
Conducting paints 167<br />
Conductivity<br />
electric 207<br />
ionic 123<br />
thermal 19 207 377 386 421 509<br />
Consolidation<br />
restoration materials 205<br />
s<strong>and</strong> 317<br />
Controlled-release<br />
drugs 304<br />
fertilizers 206<br />
Coordination catalysts 182<br />
Copolymerization<br />
cationic 187<br />
Corona discharge 482 646<br />
Corrosion<br />
problems 96 103 379<br />
resistance 12 51 203 313 378<br />
Cotackifiers 456<br />
Coupling agent 328<br />
for compatibilization 548<br />
for sisal fibers 25<br />
silane 24 161 343 658<br />
Crack front 158<br />
Crack front bowing 158<br />
Crack propagation 158<br />
Crack trapping mechanism 23<br />
Crazing 358<br />
Critical solution temperature 461<br />
Crosslinkers 472 501<br />
Crosslinking inhibitor<br />
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764<br />
Index Terms<br />
Links<br />
N,N-dimethylformamide 623<br />
Crown ethers<br />
accelerators 478<br />
polymerization retarder 187<br />
Crystallinity reduction 89 122 213 543 564<br />
Curing<br />
fluorescence response 196 381<br />
microwave 198 427 498 676<br />
ultrasonic 312<br />
Cycloaddition 317 410 495<br />
anisotropic 208<br />
Cyclocondensation<br />
phenols 248<br />
Cyclotrimerisation 379 382<br />
Cyclotrimerization 379 388<br />
Cytocompatibility<br />
polyurethane 120<br />
Cytotoxicity 687<br />
HEMA monomer 663<br />
spiroorthocarbonates 185<br />
Deep-drawing 559<br />
Degradation<br />
acid 115<br />
competitive crosslinking 53<br />
controlled rheology 618<br />
enzymatic 366<br />
glycolytic 200<br />
hydrolytic 118 431<br />
mechanism 601<br />
microbial 459<br />
photo 365<br />
thermal 21 116 387<br />
Dehydrobromination 645<br />
Dehydrochloration 148<br />
Dehydrochlorination 101 204 637 645<br />
Dehydrodecarboxylation 410<br />
Dendrimers 80 144 484<br />
Depolycondensation<br />
polyurethane 116<br />
Depolymerizable systems 488<br />
Depolymerization 45 459 526<br />
Devices<br />
electronic 164 167 211<br />
electrophotography 693<br />
medical 341<br />
optical 209<br />
photocopying 341<br />
Diacyl peroxides 36 593<br />
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765<br />
Index Terms<br />
Links<br />
Diatomaceous earth 539<br />
DiBenedetto equation 424<br />
Dicarboxylic acid<br />
a,b-unsaturated 19<br />
Dielectric analysis<br />
a-relaxation 195<br />
Dielectric loss factor 195<br />
Diels-Alder polymerization 410 428<br />
Diels-Alder reaction 15 309 400 411 434 643<br />
o-xylylene 495<br />
retro 260 313 410 433<br />
Diisocyanates<br />
blocked 79<br />
Dimer<br />
a-methyl styrene 641<br />
Dimerization<br />
isocyanates 106<br />
Dinnerware 303<br />
Dip-coating 270<br />
Discoloration 87 98 669<br />
Dispersive mixing 518<br />
Disproportionation termination 605<br />
Diterpenes 448<br />
Donor-acceptor complex 144<br />
Drug release 366<br />
Dual initiator system 28<br />
Dynamic fracture toughness 22<br />
Elasticity<br />
improvement 269 300<br />
melt 517 538<br />
Electrochromic devices 122<br />
Electrochromic windows 207<br />
Electrodeposition 203<br />
Electroless plating 215<br />
Electrolytes<br />
gel-type 207<br />
photosensitive 317<br />
solid 122 207 363<br />
Electronparamagnetic resonance 646<br />
Electrophotography 693 694<br />
Emission suppressants 11 18 255<br />
End groups<br />
amino 565<br />
carboxyl 214<br />
functionalization 569<br />
Enzymatic synthesis 84<br />
Epoxidation reaction 146 147<br />
Estrogenic activity<br />
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766<br />
Index Terms<br />
Links<br />
dental resins 687<br />
Exchanger<br />
cation 481<br />
Exfoliation<br />
nanoclays 111<br />
nanocomposites 163<br />
Exp<strong>and</strong>able graphite 33 111<br />
Explosive polymerization 190<br />
Fermentation 517 521<br />
Ferroelectric film 362<br />
Fibers 161 332<br />
Aramid 310<br />
binder 257 294 321<br />
biodegradable 521<br />
carbon 24<br />
coupling agent 161<br />
cure inhibiting 24<br />
fused-silica 96<br />
glass 23 678<br />
graphite 385<br />
insulation 267<br />
jute 25<br />
Kevlar 434<br />
mineral wool 317<br />
natural 24<br />
poly(ethylene) dyeing 646<br />
polyester 89<br />
sisal 552<br />
strength improvement 315<br />
Fillers 19 259 331 677<br />
dental 84<br />
flame retardant 378<br />
natural fibers 24<br />
plant-based 21<br />
Film blowing 524<br />
Flame retardants 31 111 168 291 356<br />
Flammability 33 303 378 501<br />
Flash point 336 600<br />
Flexibility enhancers 154<br />
Flip-chip manufacturing 206<br />
Flocculation<br />
sewage treatment 265<br />
Flory-Huggins interaction parameter 533<br />
Flow improvers 52<br />
Fluorescence response 196<br />
Fluorocarbons<br />
blowing 95<br />
Flyash 21<br />
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767<br />
Index Terms<br />
Links<br />
Foams 109 266 273<br />
ceramic 122<br />
flexible 86<br />
floral applications 266<br />
microcellular 338<br />
PET 524<br />
rigid 76 86<br />
Footwear 560<br />
Formaldehyde<br />
dispersions 257<br />
exothermic hazards 254<br />
free 275<br />
hydroxylamine titration 275<br />
low emission types 255<br />
ratio to phenol 250<br />
reduction 256<br />
resol resins 257<br />
scavengers 256<br />
Foundries<br />
furan binders 316<br />
Foundry s<strong>and</strong>s 294<br />
Fragrant oil<br />
encapsulation 304<br />
Friedel-Crafts<br />
alkylation 569<br />
catalysts 311 452<br />
reaction 405<br />
Fries rearrangement 514<br />
Furan<br />
photosensitive polymer<br />
electrolyte 317<br />
Functionalization<br />
block copolymers 542<br />
macromonomer 82<br />
montmorillonite 20<br />
of nitrile rubber 560<br />
poly(lactide) 520<br />
poly(propylene) 546 617<br />
star branched polymers 163<br />
terminating reagents 567<br />
Furniture coatings 37 47<br />
Gardner scale 458<br />
Gel coat 5 10 12 18<br />
Gel point 41 194 388 424<br />
thermal mechanical analysis 42<br />
Gelling 96<br />
catalysts 94<br />
hybride resins 30<br />
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768<br />
Index Terms<br />
Links<br />
inhibition 338<br />
preliminary 16 322<br />
reduced contraction 676<br />
viz. blowing 101<br />
Gels<br />
drug delivery system 206<br />
thermoreversible 435<br />
Glass transition temperature<br />
IPN 29<br />
modelling 153<br />
structure properties relationships 44<br />
Gloss polyesters 19<br />
Glue resins 283<br />
Graphite 694<br />
Gratings 504 644<br />
Grignard<br />
reagents 321<br />
synthesis 328<br />
Halomethylation 272<br />
Hantz reaction 284<br />
Hanza yellow 695<br />
Hardeners 176 263<br />
Hemp 23<br />
Hildebr<strong>and</strong> solubility parameter 452 455<br />
Himalaya pine 449<br />
Hindered amine light stabilizers 36<br />
Hock process 140<br />
Holography 209 644<br />
Hot-melt adhesive 459 462<br />
reactive 114<br />
Hot-melt extrusion<br />
adhesives 460<br />
Household applications 203 341 360 361 368<br />
Hydrocarbonylation<br />
ethene 353<br />
Hydrogels 205<br />
Hydroperoxides 590<br />
Hydrosilylation 328 616 643<br />
aromatic compounds 328<br />
crosslinking 335<br />
inhibitors 333<br />
platinum complexes 333<br />
silicones 199<br />
Hydrosylilation 391<br />
Ignition point<br />
peroxides 591<br />
Image<br />
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769<br />
Index Terms<br />
Links<br />
latent 693<br />
Indene resins 462<br />
Inhibitor<br />
coloring 17<br />
silicones 327<br />
trimerization 106<br />
Inhibitors<br />
anionic polymerization 480<br />
crosslinking 623<br />
grafting 623<br />
hydrosilylation 333<br />
radical polymerization 16 17 328 352 677<br />
Iniferter Method 567<br />
Initiation<br />
ultrasonic 628<br />
Initiator systems<br />
dual 676<br />
Initiators<br />
anionic 428 485<br />
atom transfer radical<br />
polymerization 461<br />
cationic 183<br />
controlled rheology 589<br />
dental polymers 669<br />
dual 28<br />
encapsulated 384<br />
functionalized 624<br />
iniferter method 567<br />
latent 186<br />
peroxide 35<br />
radical 358 387<br />
redox 658<br />
UV-sensitive 48<br />
Insertion<br />
carbene 631<br />
epoxide 182<br />
epoxy 386<br />
intercalation 162<br />
vinyl monomer 568<br />
Intercalation 162 540<br />
melt processing 109<br />
Interfacial slip 534<br />
Interlayers<br />
charged 162<br />
Intramolecular cyclization 423<br />
Intumescence 113 526<br />
Ionomers<br />
acrylic modified polyolefins 554 555<br />
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770<br />
Index Terms<br />
Links<br />
polyurethane 110<br />
Iron black 694<br />
Isocyanates<br />
comb-like 82<br />
phosgene-free synthesis 70<br />
Isomerization<br />
allyl ether 10<br />
oxazoline 386<br />
propylene oxide 87<br />
unsaturated polyester 6<br />
Jute 23 25 259<br />
Karstedt catalysts 328 333 391<br />
Keratinization 487<br />
Ketone Peroxides 36<br />
Kinetics<br />
autocatalytic curing 153 257<br />
crosslinking 117<br />
curing 40 114 166 669<br />
cyclotrimerization 389<br />
grafting 623<br />
infrared spectroscopy 423<br />
intragallery curing 163<br />
isomerization 6<br />
monitoring 193<br />
peroxide decomposition 599<br />
photopolymerization 675<br />
polyesterification 14<br />
polymerization 249<br />
self-catalyzed reaction 16<br />
water content 262<br />
Knoevenagel reaction 472<br />
Laminates<br />
continuous fibers 161<br />
hyperbranched polymers 145<br />
printed circuit boards 385<br />
Lenses 208<br />
Lignin 523<br />
Low-profile additives 21 26<br />
Lubricants 160<br />
Macroradicals 516 612 618 621 624 633<br />
poly(propylene) 547<br />
M<strong>and</strong>ioca 544<br />
Manicure compositions 486<br />
Manihot 544<br />
Manioc 544<br />
Mannich<br />
bases 179<br />
reaction 264<br />
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771<br />
Index Terms<br />
Links<br />
Marble<br />
artificial 361<br />
conservation 365<br />
Masterbatches<br />
peroxides 595<br />
Mechanochemistry 612<br />
Melt condensation 14 16<br />
Melt phase boundaries 531<br />
Membranes<br />
carbon 270<br />
dialysis 636<br />
drug release 366<br />
molecular sieves 270<br />
polyurethane 109<br />
reactive 206<br />
thermally stable 435<br />
Mercury porosimetry 543<br />
Mesomorphic phases 553<br />
Metallocene catalyst 642<br />
terminal unsaturation 569<br />
Metallocene salts 485<br />
Methylene blue 695<br />
Methylolation 286<br />
Michler’s ketone 189<br />
Microcapsules 296<br />
controlled-release of drugs 304<br />
Microcracking 44 159<br />
Microfibrils 555<br />
Microfiltration membranes 270<br />
Microgels 151 698 699<br />
Microvoids 26 44<br />
Microwave curing 197<br />
Mixer<br />
batch 53 566<br />
Brabender 550<br />
cavity transfer 612<br />
extruder 513 531<br />
Plasti-Corder 555<br />
static 612<br />
Modifiers<br />
alkenyl 374<br />
conductivity 161<br />
epoxy adhesives 203<br />
epoxy resins 112<br />
impact strength 606<br />
interphase 537<br />
liquid rubber 156<br />
melt strength 524<br />
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772<br />
Index Terms<br />
Links<br />
polyterpene resins 462<br />
tiazone 289<br />
toughness 212 290 389 417<br />
unaturated polyester 6<br />
urea resins 300<br />
Modulus<br />
compression 21<br />
elastic 121 199 377<br />
flexural 20 21 378 389 590<br />
shear 434<br />
storage 388 405 643<br />
tensile 20 45 544 553<br />
Moisture barriers 460<br />
Molecular sieve 270 522<br />
Monomer reactivity ratios 28 40 635<br />
Monoterpenes 448<br />
Multi-initiator systems 676<br />
Multiring monomers 405<br />
Multivariate analysis 196 432<br />
Müller-Rochow process 327<br />
Nail chapping 486<br />
Nanocomposites 22 532 540<br />
clay 540<br />
intercalation 20<br />
layered silicate 111 162<br />
montmorillonite 111<br />
rectorite 109<br />
silica 110<br />
silicate 377<br />
Nanofibers 678 680<br />
Nanofillers<br />
silsesquioxane 421<br />
Nanoparticles<br />
layered silicate 164<br />
metal oxide 678<br />
titanium dioxide 22<br />
Nanotubes 161<br />
Natural rubber 366 449<br />
epoxidized 22<br />
Nematic<br />
acrylics 663<br />
film 208<br />
network 146<br />
Neoprene rubber 461<br />
Network<br />
breaking 201 313<br />
hybrid 31 167<br />
interlock 29<br />
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773<br />
Index Terms<br />
Links<br />
interpenetrating 28 29 117 164 210 388<br />
429<br />
liquid crystalline 146<br />
nonazeotropic composition 40<br />
porous 435<br />
reduction of crosslink density 374<br />
reinforcement 247<br />
reversible 201<br />
silicone 331<br />
unsaturated polyester 1<br />
Nigrosine 694<br />
Nitroxides<br />
cyclic 568<br />
Nitroxyl radicals 602<br />
Nonlinear optics 209 435<br />
Novolak 142<br />
bismaleimide-modified 421<br />
cyanate ester 377<br />
diallyl bisphenol A 400<br />
epoxy resin 168 387<br />
resin 241 247<br />
thermoplastic 640<br />
toughener for 466<br />
Nucleation 304 390 551<br />
Number<br />
acid 16<br />
Avogadro 621<br />
hydroxyl 89<br />
Sherwood 510<br />
Optical applications 141 176<br />
benzocyclobutene 504<br />
Optical resins 207<br />
Organisms<br />
aquatic 344<br />
Organoclays 18 20 162<br />
Oxamides 103<br />
Ozone<br />
depletion potential 95<br />
resistance 340 461 560<br />
treatment 503<br />
Paintability 571<br />
Paper release agents 341<br />
Paraffin wax 19 455<br />
Particle collisions 538<br />
Peresters 36 595<br />
Peroxides<br />
flash points 600<br />
half-lifes 600<br />
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774<br />
Index Terms<br />
Links<br />
Phase transfer catalyst 148 514<br />
Phosgenation 73 74<br />
Phosgene<br />
reaction of bisphenol 514<br />
Phosphorylation 272<br />
Photo curing 197 485<br />
Photoalignment method 208<br />
Photochemical<br />
bromination 645<br />
chlorination 645<br />
generation of dienes 411<br />
reaction 209 317<br />
Photodimerization<br />
chalcone 208<br />
Photoinitiators 36 52 186 384 673<br />
cationic 188<br />
radical 193<br />
visible light 190<br />
Photopolymerization 30 675<br />
cationic 186 189<br />
postpolymerization 187<br />
radical 206<br />
Photoresist<br />
gratings 504<br />
negative 92 384<br />
positive 268<br />
Photostability 209<br />
Photostabilizers 681<br />
Phytotoxicity 317<br />
Pine resin 450<br />
Plasma treatment 644<br />
Plasticizers<br />
cyanoacrylate esters 475<br />
Plasticizersepoxy resins 167<br />
Polyamide 6<br />
g-crystals 551<br />
Polyesterimides 418<br />
Polymerization<br />
anionic 485<br />
coordinative 182<br />
emulsion 154 555<br />
Enthalpy 511<br />
Entropy 511<br />
furfuryl alcohol 316<br />
living 82<br />
metathesis 512<br />
multibranching 144<br />
suspension 340 696<br />
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775<br />
Index Terms<br />
Links<br />
<strong>Polymers</strong><br />
heat-resistant 110 325 342 414 428<br />
hyperbranched 144 212 412 484<br />
self-healing 296<br />
telechelic 568<br />
Polyphosphazenes 208<br />
Polyurea resins 92<br />
Polyurethane<br />
waterborne 122<br />
Postcure treatment 197 414 425 675<br />
Postpolymerization<br />
photo curing 187<br />
Pot life 17 40 42 179 182 384<br />
Pour point depressants 49 52<br />
Powder coatings 48<br />
Prepregs 386 397<br />
Pressure-sensitive adhesive<br />
hot-melt 642<br />
Primers 482 483 688<br />
Printed circuit boards 162 204 332 342 385<br />
Printing inks 186 454<br />
Printing medium<br />
ink-jet 368<br />
toner 693<br />
Promoters<br />
adhesion 615 663 682<br />
amine 29<br />
dental polymers 668<br />
redox 37<br />
silicone synthesis 327<br />
visbreaking 274<br />
Pulse-cure method 676<br />
Pyrones<br />
cycloadduct 410<br />
Quinoline yellow 695<br />
Radical<br />
b-scission 593 608<br />
branching 516<br />
chlorination 645<br />
copolymerization 40<br />
coupling 534<br />
diffusion control 29<br />
grafting 521 541 611 614<br />
grafting kinetics 623<br />
induced decomposition 627<br />
inhibitor 670<br />
initiator 34<br />
photoinitiator 186<br />
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776<br />
Index Terms<br />
Links<br />
polymerization kinetics 42<br />
scavenger 643<br />
stable 601 614<br />
telomerization 82<br />
Radical polymerization<br />
atom transfer 567 568 569<br />
bismaleimides 412<br />
chain transfer 343<br />
cyanoacrylate 485<br />
living 567<br />
ring opening 665<br />
<strong>Reactive</strong> solvents 210 246<br />
Reactors<br />
bent loop 509<br />
Recombination termination 618<br />
Reductive amination 92 104<br />
Reinforcing materials<br />
epoxides 161<br />
unsaturated polyesters 23<br />
Relaxation<br />
dipol 195<br />
viscoelastic 389<br />
Renewable resources<br />
vegetable cellulose 307<br />
Residence time 507 508 513 571 590 608<br />
613 698<br />
Resistance<br />
hydrolytic 3 90<br />
impact 22 31 554 571<br />
thermal 20 50<br />
Reworkable resins 201<br />
Rigidity control 8 44 89<br />
Ring <strong>and</strong> ball method 458<br />
Rubber tackifier 6<br />
Rutherford back-scattering technique 646<br />
Salicylates<br />
ultraviolet absorbers 356<br />
Sanitary products 47 341 361 462 558<br />
Sawdust 21 24<br />
Scaffold 119<br />
Scavengers<br />
acid 90<br />
formaldehyde 251 256<br />
Schiff bases 147<br />
Schotten-Baumann reaction 663<br />
Schulz-Flory distribution 88<br />
Scission<br />
homolytic 601<br />
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777<br />
Index Terms<br />
Links<br />
Sealants 341 460<br />
Self-extinguishing<br />
unsaturated polyesters 32<br />
Sequence length<br />
reactivity 14<br />
Sesquiterpenes 448<br />
Sewage treatment<br />
phenol/formaldehyde resins 265<br />
Shrinkage 35 42 107 198 662<br />
cationic polymerization 666<br />
control 27<br />
cyclic monomers 665<br />
low profile additive 28<br />
measurements 28<br />
strain 676<br />
Silacrown compounds<br />
preparation 478<br />
promoter 478<br />
Silaferrocenophanes 325<br />
Silly putty 321<br />
Silsequioxane resins 322<br />
Sisal 23<br />
Sizing agents 463<br />
Softening point 458 462<br />
Soil amendment 295<br />
Solubility parameters<br />
peroxides 621<br />
solvents <strong>and</strong> polymers 457<br />
Solvents<br />
aprotic 412<br />
Solvolysis 37 114 200<br />
Spin-coating 210<br />
Spoilers 517<br />
Stabilizers<br />
acid 472<br />
efficiency 622<br />
foam 340<br />
polyvinyl chloride 204<br />
storage time 79 480<br />
UV 573<br />
Starch<br />
acetylated 639<br />
amylose 639<br />
blend 522 523<br />
cassava 545<br />
corn 248 639<br />
esterification 639<br />
grafted 517 637 639<br />
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778<br />
Index Terms<br />
Links<br />
modified 523<br />
rice 629<br />
sago 544<br />
tapioca 545<br />
thermoplastic 559<br />
Steam<br />
activation 272<br />
distillation 450<br />
hydrolysis 526<br />
treatment 259<br />
Stereolithography 367<br />
Steric hindrance 14 101 166 424 425 427<br />
639<br />
Storage time<br />
inhibitors 17<br />
phenolic resin 268<br />
unsaturated polyester resin 18<br />
Strength<br />
bond 475<br />
cohesive 472<br />
compressive 13 19 267 498 663<br />
flexural 20 21 24 25 322 332<br />
384 388 389<br />
peel 156 199 385 456<br />
tensile 22 29 111 117 121 159<br />
291 389 431 435 484 544<br />
563 630<br />
Sulfonation 272<br />
Supercritical carbon dioxide 618<br />
Superglues 471<br />
Surface metallization 215<br />
Swelling<br />
chromatography support 315<br />
drug delivery system 206<br />
jute 259<br />
Syrups<br />
casting 349<br />
Tackifier 366 456<br />
Tackifying resin<br />
waterborne 460<br />
Tapes<br />
adhesive 203 342 462<br />
Tapioca 544<br />
Tempera paintings 366<br />
Tetraterpenes 448<br />
Thermal cracking 274<br />
Thermal transfer ribbons 342<br />
Thermochromic dyes 686<br />
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779<br />
Index Terms<br />
Links<br />
Thermolabile linkages 201<br />
Thermolysis 184<br />
peroxyketals 626<br />
recycling 200<br />
Thermotropic polymers 498 553<br />
Thickeners 480<br />
Thixotropic<br />
additives 18<br />
resins 13<br />
Tint agents<br />
dental polymers 659 682<br />
Tissue adhesives 487 488<br />
Toners<br />
bisphenol A fumarate 51<br />
low fix temperature 698<br />
styrene-acrylic resin 698<br />
textile printing 700<br />
Top coat 5<br />
Tougheners 212 417<br />
dendrimers 144<br />
rubbers 156<br />
Toxicity<br />
isocyanates 79<br />
maleic anhydride 622<br />
silacrown ethers 478<br />
tissue adhesives 487<br />
Transesterification 5 89 200 264 472 478<br />
515 525 554<br />
zinc acetate 45<br />
Trimerization 381<br />
Triterpenes 448<br />
Trommsdorff effect 29 42<br />
Ultrasonic<br />
assisted extrusion 532<br />
curing 312<br />
initiation 628<br />
reactor 115 <br />
Ultraviolet absorbers 36 356<br />
Ultraviolet stabilizers 36<br />
Unsaturated polyesters<br />
Π-interactions 30<br />
waterborne 10<br />
Urdiol 84<br />
Urethane dimethacrylates 84<br />
Uretonimine 77<br />
Vector fluids 549<br />
Vinyl offset 698<br />
Vinyl staining 98 105<br />
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780<br />
Index Terms<br />
Links<br />
Visbreaking 274<br />
Viscosity<br />
branched polymers 525<br />
chain stopper 668<br />
controlled rheology 590<br />
grafting 618<br />
hot-melt adhesives 462<br />
interfacial slip 534<br />
intrinsic 524 573<br />
liquid crystalline polymer 554 663<br />
reactive diluents 400<br />
thickeners 480<br />
vis-breaking processes 606<br />
Visible light sensitizer 190<br />
Vitrification 166 195 367<br />
Wagner-Jauregg reaction 425<br />
Wastewater treatment plants 519<br />
Water sorption 431 678 686<br />
Wetting agent 317<br />
Whiskers 161<br />
Xanthens 259<br />
Yucca 544<br />
Zwitterionic salts 103<br />
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