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Fig. 18.1. - - LD a 70 60 50 8 40 0 - m v) W 0 Tested at 120OOF. Solution Annealing Temperature a (OF) 23 00 2150 30 20 10 0 218 I IO 400 RUPTURE LIFE (hr) ORNL-DWG 67-3523R io00 10,000 Comparison of the Postirradiation Creep Properties of Several Hastelloy N Alloys lrra iated an Table 18.1. Effect of Aging at 1400 and 1200°F on Tensile Properties of Titanium-Modified Hastelloy N (Heat 66-548) Tensile Properties Grain Y ie Id Ultimate Total Test Condition Size Strength Strength Elongation Large No age 500 hr at 1200°F 500 hr at 1400'F Small No age 500 hr at 1200'F 500 hr at 1400'F Large No age 500 hr at 1200°F 500 hr at 1400°F Small No age 500 br at 1200°F 500 hr at 1400'F x io3 18.5 18.3 23.8 26.6 22.5 27.5 17.7 17.8 19.2 21.7 21.9 25.3 aAnnealed 2 hr at temperature. 'Large and small grain sizes resulted from the two different fabrication procedures. 'Tests wr're conducted at 1200°F in air using a strain rate of 0.05 miii.-.l. x io3 60.5 65.5 68.1 64.8 79.1 81.0 52.8 64.0 62.4 71.3 77.7 77.4 50.0 61.9 50.0 33.7 63.7 51.4 37.0 61.5 51.0 53.0 60.1 50.5
These aging studies will be expanded to include longer aging times, alloys with varying titanium and carbon levels, and complete metallographic examination to ascertain metallurgical changes. 18.3. PHASE IDENTIFICATION STUDIES IN HASTELLOY N R. E. Gehlbach The effects of thermornechanical treatments on the mechanical properties of I-Iastelloy N indicated the need for an electron microscope investigation to understand the nature of the elevated-temperature embrittlement problem. It was noticed that the transition from transgranular to intergranular failurs in the temperature range of the ductility decrease indicated probable formation of a brittle grain-boundary product - either a fine precipitate or segregation of impurity elements to grain boundaries. Preliminary examination of thinned foils by transmission electron microscopy showed precipitation occurring in the same temperature range as that of the pronounced ductility change. 'rhus a detailed study of precipitation in Hastelloy N was initiated to identify the various types, morphologies, and compositions of precipitates and to determine their relationship to the mechanical properties. Several complementary approaches are being used for the purposes of precipitate identification. Thin-foil transmission microscopy is employed for observations of fine matrix precipitate, dislocation structure, and, to a lesser extent, grain-boundary precipitate. Due to the heterogeneous nature of precipitation in Hastelloy N, sampling problems are encountered with transmission rriicroscopy. This technique is also limited in that the true nature of the precipitates is not apparent and that very thin grain-boundary films are frequently undetectable. Extraction replication techniques overcome the transmission limitations. Here, conventional metallographic specimens are lightly etched to remove the polished surface and to reveal precipitates and are then coated with a layer of carbon. Extraction replicas are obtained by heavy electrolytic etching through the carbon film, which dissolves the matrix, leaving the precipitates adhering to the carbon substrate. This permits observation of precipitates in the same distribution 219 as that existing in the bulk sample with the exception that grain-boundary precipitates are no longer supported by the matrix and collapse against the substrate as shown in Fig. 18.2. This allows direct observation of the grain-boundary precipitates on essentially the surface of the original grain boundary, providing inforiliation on true precipitate morphology and permitting examination of thin films. Identification of precipitates is simplified with extraction replicas, since interference from the matrix is eliminated. Selected area electron diffraction is being used for the identification of crystal structure and the determination of lattice parameters. Semiquantitative cornpositional analysis of individual particles is being performed using an electron probe microanalyzer accessory on one of the electron microscopes. Thus, by coordinating various approaches available in electron microscopy, precipitation processes may be studied carefully. Much of our effort has been concentrated on standard Hastelloy N. The microstructure of this material is characterized by stlingers of massive M,C carbides, the metallic constituents being primarily nickel. and molybdenum with some chromium. The carbides are very rich in silicon compared with the matrix. On aging or testing in the temperature range 1112 to 1652OF, a fine grainboundary precipitate forms (Fig. 18.2). This precipitate is also M,C with the same lattice parameter (approximately 11.0 A) as the large blocky carbides. Work is in progress to attempt to detect any compositional differences between the two morphologies of M,C carbides. Initial microprobe work using extraction replicas indicates that the grain-boundary carbides are richer in silicon than the large blocky type. All precipitates found in Hastelloy N which has not been subjected to temperatures in excess of 2372°F have been M,C carbides. When standard Hastelloy N is annealed at temperatures above about 2372OF, the M,C begins to transform to an intergranular lamellar product. Autoradiography, using 14C as a tracer, shows that this product is not a carbide and that the carbon seems to be rejected (Fig. 18.3). The blocky precipitates (Fig. 18.3) are seen to be ~ ........_.. - 3H. E. McCoy, MSR Program Semiann. Progr. Rept. Aug. 31, 1965, ORNL-3872, pp. 91-102.
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c c c Contract No. W-.740 5-eng- 26
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, INTRODUCTION ....................
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7 . SYSTEMS AND COMPONENTS DEVELOPM
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. 15.7 Oxygen Analysis ............
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i The objective of the Molten-Salt
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PART 1. MOLTEN-SALT REACTOR EXPERIM
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PART 2. MSBR DESlGN AND DEVELOPMENT
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especially when the system is stabi
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generated species in molten fluorid
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cold leg. The second loop, of Naste
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Part 1. Molten-Salt Reactor Experim
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was at full power continuously exce
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Analysis and details of operations
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1.2 REACTlVlTY BALANCE J. R. Engel
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alance results during this time sho
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II_- - 23 Table 1.2. MSRE Cumulotiv
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4 2 5 10 20 transient that followed
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27 Fig. 1.13. Motor of Reactor Cell
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personnel access to the area where
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accumulation rate at present indica
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The retrieval of the sample latch w
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The moisture condensed from the cel
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MSRE, details of some of the equipm
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39 Fig. 2.2. General View of Latch
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c 41 Table 2.1. Radiation Levels Fo
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significantly, indicating clearly t
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2.5 PUMPS P. G. Smith A. G. Grindel
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3.1 MSRE OPERATING EXPE RI ENCE C.
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The rate-of-fill interlocks, includ
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16 15 44 (3 42 I1 9 51 LLETHARGY 8
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shown as solid points in Fig. 4.1 (
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These are the results of two-dimens
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. r. ~ ~ ~ Fig. 4.8. Axiol Distribu
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. 59 Fig. 4.10. Axial Distribution
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- 12 0.0 $ 04 Lo ... z ? I- ;s -04
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Part 2. MSBR Design and Development
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ather than just the core and to pro
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A . 9.
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0 2 4 6810 LLLLLLU 1 INCHES COOLING
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however, electric heaters are provi
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I 43ft 3in REACTOR ’ t 40in. ! 3i
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of machining or close tolerances. T
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GASCONN I GAS SKIRT 4ft 8in. OD 19f
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271 TIRES 2%. A PITCH L- STEAM (la
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6.1 MSBR PHYSICS ANALYSIS 0. L. Smi
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4 V S; 0.06 v F 2.25 2.24 2.23 2.22
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0 8 6 4 7- 4=H20 SPECTRUM 2=D20 SPE
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chief indicators of performance. Th
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Work related to the Molten-Salt Bre
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I- 92 -Clt NO ClRCUl ATING BUBBLES
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L- a w r 94 ORNL-OWG 67-(1815 io‘
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about 500 mm Hg at the test operati
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1 I 1 I 1 98 MOTOR COUPLING dWER BE
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head and flow characteristics of th
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The chemical research and developme
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0 'i! m 0 w m d m w 0 W m 9 4 w lx
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Sample Nc. F312-10 FPi2-1: FP12-12
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~. 108 Table 8.2. Chemical Analyses
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tenfold or more as a consequence of
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mechanism is available which satisf
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An additional purpose of sampling w
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9. Fission Product Behavior in the
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een stripped is more nearly 50% of
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E > 0 12.0
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(014 5 2 4 o~~ 40" 5 2 5 - BLANK -~
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loi3 5 2 40’2 E : 5 m L al a 0) i
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126 Table 9.4, Fission Product Depo
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Table 9.7- Approximate Fission Prod
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(e.g., in metallic colloidal aggreg
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SAMPLES in. DlAM X t'46 in. ,,/NOR-
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c( 0 c c 0 134
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10.1 OXIDE CHEMISTRY OF ThF,-UF, ME
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BeF, in 2LiF 13eF,, this partial pr
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(up to one week) the transparency o
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The appearance in appreciable conce
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MoF3 e h l o .... ~~ .... Mo t MoF,
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i observed peak heights for Mo 2F9
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12.1 EXTRACT] ROTACTlNlUM FROM ever
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2 a STATIC -~ -0 AGITATED A AVERAGE
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to the end of the nickel anode. A m
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centration (97% removed). The distr
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point marked with a cross is the va
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13. FB u orate 13.1 PHASE RELATIONS
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THERMOCOUPI-F FURNACE I TO VACUUM O
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Cr Metal Hastelloy N Fe Mo ~ 162 Ta
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- 0 0.44 0.40 0.36 0.32 .- + z 0.28
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. Development and E aluation of for
Page 178 and 179: Sample No. M Wil 1 FP-9-4 FP-10-25
Page 180 and 181: LJ !+€AD POT I I I I I I I I 1 I
Page 182 and 183: This uranium species disappeared sl
Page 184 and 185: 174 BI I - CARRIER - ...... -+ SAMP
Page 186 and 187: olten- I rr Molten-salt breeder rea
Page 188 and 189: I COLD LEG RETURN LIN 178 CORE OUTL
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Page 192 and 193: Table 15.3. Comparison of Values fo
Page 194 and 195: likely cause of failure is the rapi
Page 196 and 197: 186 Fig. 15.6. Inner Surfoce of Col
Page 198 and 199: 188 Fig. 15.8. Inner Surface of Cor
Page 200 and 201: on final salt samples. 'This value
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Page 204 and 205: HFIR FUEL ELLEMENT ,EXPERIMEUT 194
Page 206 and 207: Our materials program has been conc
Page 208 and 209: 198 SPLIT STRAP SLEEVE BAND (a) S F
Page 210 and 211: others, but all three stringers in
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Page 214 and 215: 204 Fig. 16.7. Photomicrographs of
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Page 219 and 220: AXF-5QRG 4-4 4 a9g/rm3 4f 56 % ~ AX
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Page 223 and 224: was found. In view of the low react
Page 225 and 226: SIC TEMPERATURE STAINLESS STEEL TUB
Page 227: 18.1. IMPRQVING THE RESISTANCE are
Page 231 and 232: 221 Fig. 18.3. Hastellay N Containi
Page 233 and 234: Fig. 18.5. Hasvellcy N (Titanium Mo
Page 235 and 236: ORWL-DWG 67-tIP39 !-in -THICK PLATE
Page 237 and 238: 227 Toble 18.3. Thermal Convection
Page 239 and 240: 229 ORNL-DWG 67-io980 Impurity Anal
Page 241 and 242: 231 Fig. 18.16. Hastelloy N Thermal
Page 243 and 244: time what the effective diffusiviti
Page 245 and 246: Figure 18.20 shows an area near the
Page 247 and 248: The third design, which is also a d
Page 249 and 250: Part 6. Molten-Salt Processing and
Page 251 and 252: that the behavior of the rare-earth
Page 253 and 254: 22. Distillation of MSRE Fuel Carri
Page 255 and 256: 23. Steady-State Fission Product Co
Page 257 and 258: sec (50 hr). These latter residence
Page 259 and 260: analysis of filtered samples and th
Page 261 and 262: 25. Modifications to MSRE Fuel Proc
Page 263: nickel line through a sintered meta
Page 267 and 268: 1. R. K. Adams 2. G. M. Adamson 3.
Page 269 and 270: 344. E. H. Taylor 345. W. Terry 346
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