Packing vs. Temperature Effects in PolymersThe pioneering stu<strong>di</strong>es of Williams [1] and, morerecently, by Schug et al [2] and Paluch et al [3]pointed out that a deeper insight into the dynamicsof glass-forming liquids and amorphous polymers isgained by the knowledge of the relaxation times as afunction of both temperature and pressure. In fact,the possibility to reach the glassy state by twoalternative paths, i.e., by cooling or compressing,enables a more stringent test of several theories,which usually pre<strong>di</strong>ct a Vogel–Fulcher kind ofbehavior for the temperature dependence of therelaxation time but <strong>di</strong>fferent pressure dependencies.We have performed a molecular dynamics simulationFig. 1: The pressure-temperature dependence ofthe segmental relaxation time for a linear polymermodel. The inset shows the pressure dependence ofthe ratio between the isobaric and isochronicexpansivities.of a melt of unentangled polymers [4]. Thetranslational motion, the large-scale and the localreorientation processes of the chains, as well as theirrelations with the so-called ‘‘normal’’ and‘‘segmental’’ <strong>di</strong>electric relaxation modes arethoroughly investigated in wide temperature andpressure ranges (Figure 1). The study addresses theissue whether the temperature or the density is adominant control parameter of the dynamics or thetwo quantities give rise to comparable effects. Byexamining the ratio between the isochronic an<strong>di</strong>sobaric expansivities, one finds that the temperatureis dominant when the dynamics is fast. If therelaxation slows down, the fluctuations of the freevolume increase their role and become comparableto those of the thermal energy.The role of packing effects has been alsoinvestigated by addressing the issue of the finitelength of polymer chains which affects both the staticand the relaxation properties of the density of themelt state [5]. These have been investigated bymolecular-dynamics simulations of a Lennard-Jonesmodel with fixed bond length. Under isothermal–isobaric con<strong>di</strong>tions the density increases with themolecular weight. A suitable Voronoi tessellationreveals the extra free volume around the chain endsand shows that it is strongly localized within the firstend monomer (Figure 2). Simple arguments aregiven for interpreting the main changes of themonomer ra<strong>di</strong>al <strong>di</strong>stribution function and thecorrespon<strong>di</strong>ng static structure factor when the chainlength is increased. As to the relaxationaspects of the density, it is found that the structuralrelaxation time increases with the molecular weight,which is interpreted as a signature of the well-knowncorrespon<strong>di</strong>ng increase of the glass transitiontemperature.References[1] G. Williams, Trans. Faraday Soc. 60, 1548(1964).[2] K. U. Schug, H. E. King, R. Böhmer, J. Chem.Phys. 109, 1472 (1998).[3] M. Paluch, A. Patkowski, E. Fischer, Phys. Rev.Lett. 85, 2140 (2000).[4] A.Barbieri, S.Capaccioli, E.Campani and D.Leporini, J.Chem.Phys., 120, 437 ( 2004 ).[5] A Barbieri, D.Prevosto, M.Lucchesi and DLeporini,J. Phys.: Condens. Matter, 16, 6609 (2004).Fig. 2: The average volume of the Voronoipolyhedra around the monomers located at the nposition along the chain with length M. Note thelarger volume of the polyhedra surroun<strong>di</strong>ng thechain-ends ( n = 1).AuthorsA. Barbieri(a), E. Campani(a,b), S. Capaccioli(a,b),D. Leporini(a,b), M.Lucchesi (a,c)(a) <strong>Dipartimento</strong> <strong>di</strong> <strong>Fisica</strong> ‘‘Enrico Fermi,’’ Universita`<strong>di</strong> Pisa, via F. Buonarroti 2, I-56127 Pisa, Italy (b)CRS-SOFT (c) Dip. <strong>Fisica</strong> “E. Fermi” Univ. Pisa andCNR-INFM Polylab Largo B. Pontecorvo 3, Pisa.55SOFT Scientific <strong>Report</strong> 2004-06
Scientific <strong>Report</strong> – Non Equilibrium Dynamics and ComplexityA Manifestation of the Ostwald Step Rule: The Free-EnergyLandscape of Single-Molecule Polyethylene CrystalsFolded states of chainlike macromolecules inclu<strong>di</strong>ngproteins [1] and crystalline polymers [2] are undercurrent intense study. In spite of the large<strong>di</strong>fferences between homopolymers and proteins,interesting correspondences between the structuraltransitions of isolated, single homopolymer chainsand the protein fol<strong>di</strong>ng have been noted by bothnumerical simulations and experiments. One keyissue is if the morphologies of folded states arethermodynamically or kinetically controlled. Kineticfactors are believed to set the growth rate ofpolymer crystals [2] as well as the thickening offolded macromolecules. While this is a safeconclusion for long chains (polymers) , where largeFig. 1: (left) Snapshots of the crystallization of asingle PE chain with N=500 monomers. Note thepresence of initial <strong>di</strong>stinct nucleation sites mergingat later times. (right) Final crystal structure withselected cross-sections.entropic barriers hamper the conformation changeslea<strong>di</strong>ng to structures which are, e.g., partiallycrystalline, it may be questioned for shorter chains(oligomers) which are less impeded.Extensive molecular-dynamics simulations of thecrystallization process of a single polyethylene chain( PE ) with N=500 monomers have been performed[4-6]. The development of the ordered structure isseen to proceed along <strong>di</strong>fferent routes involvingeither the global reorganization of the chain or,alternatively, well-separated connected nuclei(Figure 1). No dependence on the thermal historywas observed at the late stages of the crystallization.The fol<strong>di</strong>ng process involves several interme<strong>di</strong>ateordered metastable states, in strong analogy withthe experiments, and ends up in a well-defined longlivedlamella with ten stems of approximately equallength, arranged into a regular, hexagonal pattern(Figure 1). This behavior may be seen as amanifestation of the Ostwald step rule [3]. Both themetastable states and the long-lived one areevidenced as the local minima and the global one ofthe free-energy landscape (FEL), respectively (Figure2) [4,5]. The study of the microscopic organizationof the lamella evidenced that the two caps are ratherflat, i.e., the loops connecting the stems are short.Interestingly, annealing the chain through the<strong>di</strong>fferent metastable states leaves the averagenumber of monomers per loop nearly unchanged [6].It is also seen that the chain ends, the so-called cilia,are localized on the surface of the lamella, inagreement with the experiments, and that structuralfluctuations take place on the lamella surface.References[1] M. Gruebele, Annu. Rev. Phys. Chem., 50, 485(1999).[2] G. Ungar, J. Stejny, A. Keller, I. Bidd, and M. C.Whiting, Science 229, 386 (1985).[3] W. Ostwald, Z. Phys. Chem., Stoechiom.Verwandtschaftsl. 22, 289 (1897).[4] L Larini, A Barbieri, D Prevosto, P A Rolla and DLeporini, J. Phys.: Condens. Matter, 17, L199(2005).[5] L Larini, D Leporini, J.Chem.Phys., 123, 144907( 2005 ).[6] L Larini, A Barbieri D Leporini, in press onPhysica A ( doi:10.1016/j.physa.2005.08.048 )Fig. 2: (left) Free-energy landscape ( FEL ) of thePE single-molecule crystals. (right) FEL at <strong>di</strong>fferenttemperatures as a function of the largest momentof inertia of the chain. The labels in<strong>di</strong>cate thenumber of stems of the ordered structurescorrespon<strong>di</strong>ng to the minima.AuthorsA.Barbieri(a), D.Prevosto (a), L.Larini (a,b),D.Leporini (a,b), P.A.Rolla (a)(a) <strong>Dipartimento</strong> <strong>di</strong> <strong>Fisica</strong> ‘‘Enrico Fermi,’’ Universita`<strong>di</strong> Pisa, via F. Buonarroti 2, I-56127 Pisa, Italy (b)CRS-SOFT (c) Dip. <strong>Fisica</strong> “E. Fermi” Univ. Pisa andCNR-INFM Polylab Largo B. Pontecorvo 3, Pisa.SOFT Scientific <strong>Report</strong> 2004-0656
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