Characterization and control of the fiber-matrix interface in ceramic ...

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ORNL/TM-11039 Metals and Ceramics Division CHARACTERIZATION AND CONTROL OF THE FIBER-MATRIX INTERFACE IN CERAMIC MATRIX COMPOSITES R. A. Lowden Date Published: March 1989 Prepared for the DOE Office of Fossil Energy AA 1.5 10 10 0 Prepared by the OAK RIDGE NATIONAL LABORATORY Oak Ridge, Tennessee 37831-6285 operated by MARTIN MARIETTA ENERGY SYSTEMS, INC. for the U.S. DEPARTMENT OF ENERGY under Contract DE-ACOS-840R21400 3 4456 0290b45 2
Page 5 and 6: TABLE OF CONTENTS Page LIST OF TABL
Page 7: Page 11.3 Interfacial Frictional St
Page 11 and 12: LIST OF FIGURES Figure Page 4.1. Sc
Page 13 and 14: Figure Page 10.7. SEM micrographs s
Page 15: Figure Page 11.5. The diffusion coe
Page 18 and 19: Strengthening with fibers has so ma
Page 20 and 21: 2 chemical interactions at the inte
Page 23 and 24: 2. HISTORICAL DEVELOPMENTS IN CERAM
Page 25: 7 Although these materials did not
Page 28 and 29: 10 lay-ups or filaiiients wound int
Page 30 and 31: 12 plates or complex shapes contain
Page 33 and 34: 4. FORCED-FLOW THERMAL-GRADIENT CHE
Page 35: 17 materials and certain ceramic-fi
Page 38 and 39: 20 Table 5.1. Properties of some re
Page 40 and 41: 22 of the composite and the contrib
Page 42 and 43: 24 Therefore, the maximum strength
Page 44 and 45: 26 was derived from extensive testi
Page 46 and 47: 28 ORNL-DWG 138-9023 Figure 5.2. Th
Page 48 and 49: 30 The stress in the matrix resulti
Page 50 and 51: 32 reinforcement w Lll be lost. 'Th
Page 52 and 53:
34 The selection of the coinponents
Page 55 and 56:
6. FIBER-MATRIX INTERFACES 6.1 Intr
Page 57 and 58:
39 ORNL-DWG 89-2156 F F y-CCACM COA
Page 59 and 60:
41 I. 2 I .o 0. e c.. - l! O6 v) Ru
Page 61 and 62:
.43 matrix in a composite will begi
Page 63 and 64:
7. CHARACTERIZATION OF THE FIBER-MA
Page 65 and 66:
47 F - 2nRtr , where r is the frict
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49 in Figure 7.2. Based on the mult
Page 69 and 70:
51 ORNL-DWG 88-7f 25 FIBER + I I -J
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53 shorter lengths. Fragmentation o
Page 73 and 74:
55 The multiple-matrix fracture con
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57 ORNL-DWG 87-48230 SINGLE FRACTUR
Page 77 and 78:
59 determined by the difference in
Page 79 and 80:
8. CONTROLLING THE INTERFACE 8.1 In
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63 ORNL PBOTO 6676-86 Figure 8.2. F
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66 bonding. Low-modulus or "soft" m
Page 86 and 87:
68 providing a compliant coating th
Page 88 and 89:
70 ORNL-DWG 88-14864R rSlGHT PORT F
Page 90 and 91:
72 GRAFOIL ""'7 PERFORATED L'D-7 --
Page 92:
QRNL BWG 87-15308R SCRUBBER COLUMN
Page 95 and 96:
77 was not deoxygenated. Other gase
Page 97 and 98:
79 Y201840 Y201841 Figure 9.5. Grap
Page 99 and 100:
81 Table 9.1. Precoating processing
Page 101 and 102:
83 9.4 Mechanical ProDerties 9.4.1
Page 103 and 104:
85 true tensile strength of a compo
Page 105 and 106:
87 .. h 8 o La z 4J u 4 k 4 4
Page 107 and 108:
89 cut surface. This alignment is e
Page 109 and 110:
91 YP5199 YP5200 *I Figure 9.8. Pho
Page 111 and 112:
93 the cracks. In addition, if the
Page 113 and 114:
10. RESULTS 10.1 ComDosite ProDerti
Page 116 and 117:
98 Table 10.1. Property summary for
Page 118 and 119:
100 Table 10.2. Interfacial frictio
Page 120 and 121:
, - - I e-, 75 ORNL-DWG 87-15948R C
Page 122 and 123:
I 104 I I 1 I rr) '0
Page 124 and 125:
OANL-DWC 88-6289 I I I I I I I I I
Page 126 and 127:
108 A rl A r
Page 128 and 129:
110 steps demonstrates that silicon
Page 130 and 131:
112 t Figure 10.8. The presence of
Page 132 and 133:
114 c Figure 10.10. SEM micrograph
Page 134 and 135:
116 Table 10.5. Thermochemical eval
Page 136 and 137:
118 microprobe was not equipped to
Page 138 and 139:
350 300 CVI- 175 RAT. 175201 I 250
Page 140 and 141:
122 (N) OVOl
Page 142 and 143:
Page 144 and 145:
126 predicted weight loss was 3%. T
Page 146 and 147:
I F Figure 10.17. SEM micrographs o
Page 148 and 149:
3 130 87 1 I I .C b Y --Q) -w -e -N
Page 150 and 151:
Page 153 and 154:
ORNL-OW 88-6289 ORNL-Dwc 88-6294 BU
Page 155 and 156:
137 Table 10.8. Boron nitride coati
Page 157 and 158:
139 RAL 102744 Figure 10.23. SEM mi
Page 159 and 160:
141 infiltration by the preferred p
Page 161 and 162:
143 YP 4971 YP 4970 Figure 10.25. C
Page 163:
1 $1 0 *- QI 12 U 8 Pl 145 1 $1 0 T
Page 166 and 167:
148 The resultant fibers are compos
Page 168 and 169:
150 Table 11.1. Properties of Sic.
Page 170 and 171:
152 Table 11.2. The influence of in
Page 172 and 173:
154 11.2.2 Fracture stress and Youn
Page 174 and 175:
156 ORNL-DWG 88-6276 MATRIX CRACKIN
Page 176 and 177:
158 As previously discussed, the ul
Page 178 and 179:
160 Fiber length becomes important
Page 180 and 181:
162 upon matrix failure. This is th
Page 182 and 183:
164 ORNL-DWG 88-747iR -10 -12 -4 4
Page 184 and 185:
as-received fibers have a slightly
Page 186 and 187:
168 throughout the composite sample
Page 188 and 189:
170 SHEAR STRESS, T(MPo) 2 4 6 8 IO
Page 190 and 191:
172 failure and extensive fiber pul
Page 192 and 193:
174 Conversely, the individual Nica
Page 194 and 195:
176 I 3D Figure 11.7. Stress blocks
Page 197 and 198:
12. CONCLUSIONS AND mTTURE WORK Fab
Page 199 and 200:
REFERENCES 1. A. H. Cotrell, "Stron
Page 201 and 202:
183 31. J. C. Whithers, "Chemical V
Page 203 and 204:
185 56. E. Ryskewitch, "Compressive
Page 205 and 206:
187 85. J. F. Mandell, K. C. C. Hon
Page 207 and 208:
Part I' 189 111. W. V. Kotlensky, "
Page 209 and 210:
191 140. D. P. Stinton and W. J. La
Page 211:
APPENDIX A AUGER ELECTRON SPECTROSC
Page 214 and 215:
196 Table A-1. Auger spectral peaks
Page 217 and 218:
APPENDIX B. DETAILS OF' THE FIBER-S
Page 219 and 220:
QRNL/TM-11039 INTERNAL DISTRIBUTION
Page 221 and 222:
203 109-110. BATTELLE COLUMBUS LABO
Page 223 and 224:
205 150-152. LAJESXIDE CORPORATION,
Page 225 and 226:
207 189. 190. 191. 192. 193. 194. 1
Page 227:
209 218. DOE, OAK RIDGE OPERATIONS,
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