Journal of Nuclear Materials 386-388(2009)643-646 Contents lists available at ScienceDirect Journal of Nuclear materials ELSEVIER journalhomepagewww.elsevier.com/locate/jnucmat Microstructure and mechanical properties of silicon carbide fiber-reinforced silicon carbide composite fabricated by electrophoretic deposition and hot-pressing Katsumi Yoshida, Kozue Matsukawa, Toyohiko Yano Research Laboratory for Nuclear Reactors, Tokyo Institute of Technology 2-12-1, O-okayama, Meguro-ku, Tokyo 152-8550, Japan A BSTRACT Colloidal graphite aqueous solution was used as the su on for carbon coating on the fiber and car- bon layer was formed on SiC fiber by electrophoretic method, and Sic/Sic composite was fabricated by sheet stacking method and hot-pressing. The effect of the concentration of colloidal graphite on mechan- cal properties of SiC/SiC composite was investigated. Bulk density and open porosity of the composite fabricated in this study were nearly the same, and these values were independent of the concentration of olloidal graphite suspension. The carbon coating on SiC fibers was successfully formed by the electro- phoretic deposition method using colloidal graphite suspension. In the case of coating with 0. 10mass% of colloidal graphite suspension on Sic fibers, relatively uniform carbon coating on the fibers was observed and large fiber pullout occurred effectively during fracture. e 2008 Elsevier B V. All rights reserved. 1 Introduction has been developed and it shows electric conductivity due to its high crystallinity. We have paid attention to electric properties of Silicon carbide(Sic) is an attractive material for future fusion polycrystalline SiC fiber, and electrophoretic deposition method reactors since it has low induced radioactivity quick decay of has been applied for the formation of carbon layer on the fiber ctivity, low heat evolution after neutron irradiation, low atomic and the Sic matrix between each fiber filaments [21 In our pre number, good fracture resistance, excellent high-temperature ous study, we have successfully achieved the formation of carbon mechanical and thermal properties and corrosion resistance [1- layer on Sic fiber by electrophoretic deposition method using 6. Furthermore, Sic shows good resistance to high-energy neutron carbon black suspension 21 irradiation up to very high neutron fluences [7-11. However, In this study, colloidal graphite aqueous solution was used as monolithic Sic ceramics show a brittle fracture behavior and low the suspension for carbon coating on the fiber and carbon layer fracture toughness, and the application of SiC ceramics as the com- was formed on Sic fiber by electrophoretic deposition method, ponents has been limited due to its low reliability. In order to over- and Sic/Sic composite was fabricated by sheet stacking method come this problem, Sic fiber-reinforced Sic composite(SiC/SiC), and hot-pressing. Microstructure and mechanical properties of rhich shows a non-brittle fracture behavior and higher fracture Sic/Sic composites were evaluated, and the effect of the concentra- energy, has been studied. Future fusion power reactor concepts tion of colloidal graphite on mechanical properties of Sic/Sic based on the use of Sic/SiC composite have been designed by JA (DREAM reactor)[12]. ARIES team (ARIES-L IV and AT)[13-15] and CEA (TAURO)[16]. 2. Experimental proce The authors have explored a new fabrication process using sheet stacking method and hot-pressing in order to simplify the 2.1. Preparation of carbon and Sic coated Tyranno SA cloth abrication process and to obtain dense composite with higher mechanical and thermal properties [17-20]. The dense composite wo dimensionally plain-woven Tyranno SA(SiC fiber, Ube with a non-brittle fracture behavior could be obtained by this pro- Industries, Japan)cloth was used as the reinforcement Sizing agent ss. Formation of carbon or boron nitride layer on the fiber and on the cloth was removed by hot water. The cloth was cut into the the Sic matrix between each fiber filament is one of the most size of 35 x 35 mm square. The suspension of graphite factors to improve the mechanical properties of the was prepared using a colloidal graphite aqueous solution Recently, polycrystalline SiC fiber(Tyranno SA) Hitachi Powdered Metals, Japan), and the concentration of ce th and excellent heat resistance at high temperatures graphite was adjusted to 0.05, 0.10 and 0.50mass%. The ph of this suspension was adjusted to 10 using small amount of n-butyl- 4 Corres amine. The cloth and graphite plate were settled at a distance of E-mail address: k-yoshida@nr titechac jp(K. Yoshida 10 mm in the colloidal graphite suspension as the anode and the 0022-3115/s- see front matter o 2008 Elsevier B.V. All rights reserved. doi:10.1016 nuchal.20082314
Microstructure and mechanical properties of silicon carbide fiber-reinforced silicon carbide composite fabricated by electrophoretic deposition and hot-pressing Katsumi Yoshida *, Kozue Matsukawa, Toyohiko Yano Research Laboratory for Nuclear Reactors, Tokyo Institute of Technology 2-12-1, O-okayama, Meguro-ku, Tokyo 152-8550, Japan article info abstract Colloidal graphite aqueous solution was used as the suspension for carbon coating on the fiber, and carbon layer was formed on SiC fiber by electrophoretic method, and SiC/SiC composite was fabricated by sheet stacking method and hot-pressing. The effect of the concentration of colloidal graphite on mechanical properties of SiC/SiC composite was investigated. Bulk density and open porosity of the composites fabricated in this study were nearly the same, and these values were independent of the concentration of colloidal graphite suspension. The carbon coating on SiC fibers was successfully formed by the electrophoretic deposition method using colloidal graphite suspension. In the case of coating with 0.10mass% of colloidal graphite suspension on SiC fibers, relatively uniform carbon coating on the fibers was observed and large fiber pullout occurred effectively during fracture. 2008 Elsevier B.V. All rights reserved. 1. Introduction Silicon carbide (SiC) is an attractive material for future fusion reactors since it has low induced radioactivity, quick decay of activity, low heat evolution after neutron irradiation, low atomic number, good fracture resistance, excellent high-temperature mechanical and thermal properties and corrosion resistance [1– 6]. Furthermore, SiC shows good resistance to high-energy neutron irradiation up to very high neutron fluences [7–11]. However, monolithic SiC ceramics show a brittle fracture behavior and low fracture toughness, and the application of SiC ceramics as the components has been limited due to its low reliability. In order to overcome this problem, SiC fiber-reinforced SiC composite (SiC/SiC), which shows a non-brittle fracture behavior and higher fracture energy, has been studied. Future fusion power reactor concepts based on the use of SiC/SiC composite have been designed by JAERI (DREAM reactor) [12], ARIES team (ARIES-I, IV and AT) [13–15] and CEA (TAURO) [16]. The authors have explored a new fabrication process using sheet stacking method and hot-pressing in order to simplify the fabrication process and to obtain dense composite with higher mechanical and thermal properties [17–20]. The dense composite with a non-brittle fracture behavior could be obtained by this process. Formation of carbon or boron nitride layer on the fiber and the SiC matrix between each fiber filament is one of the most important factors to improve the mechanical properties of the composite. Recently, polycrystalline SiC fiber (Tyranno SA) with high strength and excellent heat resistance at high temperatures has been developed, and it shows electric conductivity due to its high crystallinity. We have paid attention to electric properties of polycrystalline SiC fiber, and electrophoretic deposition method has been applied for the formation of carbon layer on the fiber and the SiC matrix between each fiber filaments [21]. In our previous study, we have successfully achieved the formation of carbon layer on SiC fiber by electrophoretic deposition method using carbon black suspension [21]. In this study, colloidal graphite aqueous solution was used as the suspension for carbon coating on the fiber, and carbon layer was formed on SiC fiber by electrophoretic deposition method, and SiC/SiC composite was fabricated by sheet stacking method and hot-pressing. Microstructure and mechanical properties of SiC/SiC composites were evaluated, and the effect of the concentration of colloidal graphite on mechanical properties of SiC/SiC composite was investigated. 2. Experimental procedures 2.1. Preparation of carbon and SiC coated Tyranno SA cloth Two dimensionally plain-woven Tyranno SA (SiC fiber, Ube Industries, Japan) cloth was used as the reinforcement. Sizing agent on the cloth was removed by hot water. The cloth was cut into the size of 35 35 mm square. The suspension of graphite particles was prepared using a colloidal graphite aqueous solution (Hitasol, Hitachi Powdered Metals, Japan), and the concentration of colloidal graphite was adjusted to 0.05, 0.10 and 0.50mass%. The pH of this suspension was adjusted to 10 using small amount of n-butylamine. The cloth and graphite plate were settled at a distance of 10 mm in the colloidal graphite suspension as the anode and the 0022-3115/$ - see front matter 2008 Elsevier B.V. All rights reserved. doi:10.1016/j.jnucmat.2008.12.314 * Corresponding author. E-mail address: k-yoshida@nr.titech.ac.jp (K. Yoshida). Journal of Nuclear Materials 386–388 (2009) 643–646 Contents lists available at ScienceDirect Journal of Nuclear Materials journal homepage: www.elsevier.com/locate/jnucmat
K Yoshida et al. /Journal of Nuclear Materials 386-388(2009)643-646 cathode, respectively the cloth was coated with graphite by elec- rectangular bars(3 mmx 2 mm' x 35 mm). Bulk density was trophoretic deposition under an applied voltage of 3 V for 10 min, measured by Archimedes' method. Three-point bending strength nd then dried at 100C. The 10mass% of B-SiC aqueous suspension was measured at room temperature with a span of 30 mm and a (Ibiden, Japan) with sintering aids(20mass% in total)with a-Al2O3 crosshead speed of 0. 1 mm/min The number of test pieces in each aimei Chemicals, Japan), Y203(High Purity Chemical, Japan) and specimen for bending test was 4-5. Bending strength was calcu CaO (Kanto Chemical, Japan) was also prepared using pure water lated from the maximum load for fracture. Microstructu amine. The cloth coated with graphite was dipped into the Sic ma- scanning electron microscope(FE-SEM/erved by a field emission and the ph of the suspension was adjusted to 10 using n-butyl- fracture surface of the composite were ob trix component suspension, and electrophoretic deposition was performed under an applied voltage of 5 V for 20 min, and then 3 Results and discussion the coated cloth was dried at 100oC. The fiber volume fraction of SiC/SiC composite fabricated in this on of study was 48.8-59.5%. Table 1 lists bulk density and open porosity of Sic/Sic composites fabricated in this study. Bulk density an The slurry for tape casting was prepared using B-SiC powder, open porosity of the composites were 2.8-2.9 g/cm and 8.5- tering aids(20mass% in total)using a-Al203. Y203 and Cao, 9.3%, respectively. These values were nearly the same and indepen- tory-scale tape casting equipment(DP150, Tsugawa Seiki, Japan). shows SEM micrographs of the cross section of the Sic/sic compos- Details of the composition, organics in the green sheet were de- ites obtained in this study. In the case of the composites using Sic scribed in Ref. [17]. The thickness of the Sic green sheet was fibers coated with 0.05mass% and 0.10mass% of colloidal graphite approximately 40-50 um. The Sic green sheet was cut into the size suspension, carbon and Sic phases between SiC fibers were ob- served. However, only carbon phase was observed between Sic fl bers in the composite using Sic fibers coated with 0.50mass% of 2.3. Fabrication and evaluation of sic/sic composite colloidal graphite suspension. Most of pores existed between each fiber filament whereas the Sic matrix was so dense. Fig. 2 shows The cloths coated with carbon and the Sic matrix component, the typical load-crosshead displacement curves of Sic/Sic cor nd the Sic green sheets were stacked alternately. The stacked ites in bending test at room temperature, and bending strength of body was heat-treated at 300C for 24 h in air under a uniaxial Sic/SiC composites is listed in Table 1. Average bending strength of pressure of 20 kPa in order to remove organics such as binder from the composite using Sic fibers coated with 0.05mass8, 0.10mass% the green sheets. The compact was hot-pressed at 1700C for 1 h and 0. 50mass% of colloidal graphite suspension was 132, 117 and in Ar under a uniaxial pressure of 40 MPa. Specimens were cut into 108 MPa, respectively. Bending strength of the composite gradu ally decreased with an increase in the concentration of colloidal graphite suspension. The composite using SiC fibers coated with 0.05mass% of colloidal graphite suspension showed a stepwise vior. In the case of the composite using SiC fibers Bulk density, open porosity and bending strength of Sic/sic composites using Sic coated with 0.10mass% of colloidal graphite suspension, the load fibers coated with gradually decreased with increasing the crosshead displacement The concentration of colloidal Bulk density Open porosity Bending strength after reachi graphite suspension(mass%) (g/cm) after reaching maximum load. In the case of the composite using SiC fibers coated with 0.50mass% of colloidal graphite suspension, the load suddenly dropped after reaching the maximum load, and 9.32 8.52 then the load slightly decreased with an increase in crosshead displacement. b 50m Fig. 1. SEM micrographs of the cross section of SiC/SiC composites using SiC fibers coated with various concentration of colloidal graphite suspension. The concentration of colloidal graphite suspension was(a)0.05, (b)0.10 and (c)0.50mass%
cathode, respectively. The cloth was coated with graphite by electrophoretic deposition under an applied voltage of 3 V for 10 min, and then dried at 100 C. The 10mass% of b-SiC aqueous suspension (Ibiden, Japan) with sintering aids (20mass% in total) with a-Al2O3 (Taimei Chemicals, Japan), Y2O3 (High Purity Chemical, Japan) and CaO (Kanto Chemical, Japan) was also prepared using pure water and the pH of the suspension was adjusted to 10 using n-butylamine. The cloth coated with graphite was dipped into the SiC matrix component suspension, and electrophoretic deposition was performed under an applied voltage of 5 V for 20 min, and then the coated cloth was dried at 100 C. 2.2. Fabrication of SiC green sheet The slurry for tape casting was prepared using b-SiC powder, sintering aids (20mass% in total) using a-Al2O3, Y2O3 and CaO, and some organics. The SiC sheet was prepared using a laboratory-scale tape casting equipment (DP150, Tsugawa Seiki, Japan). Details of the composition, organics in the green sheet were described in Ref. [17]. The thickness of the SiC green sheet was approximately 40–50 lm. The SiC green sheet was cut into the size of 35 35 mm square. 2.3. Fabrication and evaluation of SiC/SiC composite The cloths coated with carbon and the SiC matrix component, and the SiC green sheets were stacked alternately. The stacked body was heat-treated at 300 C for 24 h in air under a uniaxial pressure of 20 kPa in order to remove organics such as binder from the green sheets. The compact was hot-pressed at 1700 C for 1 h in Ar under a uniaxial pressure of 40 MPa. Specimens were cut into rectangular bars (3 mmw 2 mmt 35 mml ). Bulk density was measured by Archimedes’ method. Three-point bending strength was measured at room temperature with a span of 30 mm and a crosshead speed of 0.1 mm/min. The number of test pieces in each specimen for bending test was 4–5. Bending strength was calculated from the maximum load for fracture. Microstructure and fracture surface of the composite were observed by a field emission scanning electron microscope (FE-SEM). 3. Results and discussion The fiber volume fraction of SiC/SiC composite fabricated in this study was 48.8–59.5%. Table 1 lists bulk density and open porosity of SiC/SiC composites fabricated in this study. Bulk density and open porosity of the composites were 2.8–2.9 g/cm3 and 8.5– 9.3%, respectively. These values were nearly the same and independent of the concentration of colloidal graphite suspension. Fig. 1 shows SEM micrographs of the cross section of the SiC/SiC composites obtained in this study. In the case of the composites using SiC fibers coated with 0.05mass% and 0.10mass% of colloidal graphite suspension, carbon and SiC phases between SiC fibers were observed. However, only carbon phase was observed between SiC fi- bers in the composite using SiC fibers coated with 0.50mass% of colloidal graphite suspension. Most of pores existed between each fiber filament whereas the SiC matrix was so dense. Fig. 2 shows the typical load-crosshead displacement curves of SiC/SiC composites in bending test at room temperature, and bending strength of SiC/SiC composites is listed in Table 1. Average bending strength of the composite using SiC fibers coated with 0.05mass%, 0.10mass% and 0.50mass% of colloidal graphite suspension was 132, 117 and 108 MPa, respectively. Bending strength of the composite gradually decreased with an increase in the concentration of colloidal graphite suspension. The composite using SiC fibers coated with 0.05mass% of colloidal graphite suspension showed a stepwise fracture behavior. In the case of the composite using SiC fibers coated with 0.10mass% of colloidal graphite suspension, the load gradually decreased with increasing the crosshead displacement after reaching maximum load. In the case of the composite using SiC fibers coated with 0.50mass% of colloidal graphite suspension, the load suddenly dropped after reaching the maximum load, and then the load slightly decreased with an increase in crosshead displacement. Table 1 Bulk density, open porosity and bending strength of SiC/SiC composites using SiC fibers coated with various concentration of colloidal graphite suspension. The concentration of colloidal graphite suspension (mass%) Bulk density (g/cm3 ) Open porosity (%) Bending strength (MPa) 0.05 2.88 8.73 132 0.10 2.75 9.32 117 0.50 2.90 8.52 108 Fig. 1. SEM micrographs of the cross section of SiC/SiC composites using SiC fibers coated with various concentration of colloidal graphite suspension. The concentration of colloidal graphite suspension was (a) 0.05, (b) 0.10 and (c) 0.50mass%. 644 K. Yoshida et al. / Journal of Nuclear Materials 386–388 (2009) 643–646
K. Yoshida et aL /Journal of Nuclear Materials 386-388(2009 )643-646 645 0.1mm 1mm Crosshead displacement (a u. Fig. 2. The typical load-displacement curves of Sic/siC co b coated with various concentration of colloidal graphite suspension in bending test temperature. The concentration of colloidal graphite suspension was(a 005,(b)0.10and(c)0.50mass% SEM micrographs of the fracture surface of the composites ob- served from the tensile surface after bending test were shown in Fig 3. The composite using Sic fibers coated with 0.05mass% of col idal graphite suspension exhibited short fiber pullout, and frac- ture surface was almost flat. In the case of the composite using SiC fibers coated with 0.10mass% of colloidal graphite suspension, large fiber pullout was observed. The fracture surface of the com- 1 mm posite using SiC fibers coated with 0.50mass% of colloidal graphit uspension was stepwise and showed large fiber pullout. In order to investigate the effect of carbon coating on the sic fi- ber on bending strength and fracture behavior of the composite, the carbon coating of Sic fiber after electrophoretic deposition was observed by SEM. SEM micrographs of the surface of SiC fibers coated with colloidal graphite suspension by electrophoretic depo- ition method are shown in Fig 4 Carbon existed sparsely on the surface of Sic fiber coated with 0.05mass% of colloidal graphite suspension, i.e., carbon was coated non-uniformly on the fiber. It is indicated that the interface between the fber and the matrix was not uniform and fiber pullout did not occur easily during frac- ture. As a result, the composite using Sic fibers coated with 0.05mass% of colloidal graphite suspension showed higher bending strength than the composites using Sic fibers coated with 1mm 0.10mass% and 0.50mass% of colloidal graphite suspension because Fig 3 SEM micrographs of the fracture surface of SicSic composites iC the interface between the fiber and the matrix did not act effec fibers coated with various concentration of colloidal graphite suspension tively and showed higher friction during fracture. Furthermore, from the tensile surface after bending test. The concentration of colloidal graphite the difficulty in fiber pullout during fracture caused a stepwise suspension was(a)0.05.(b)0.10 and (e)0.50massk fracture behavior and almost flat fracture surface with short fiber pullout. In the case of coating with 0. 10mass% of colloidal graphite the composite, it seemed that the optimal interface between the fi- was 0. 10mass% in this study ber and the matrix was obtained by the electrophoretic deposition under this condition. In the case of coating with 0.50mass% of col- 4 Summary lodal graphite suspension, carbon layer on the Sic fiber was so thick compared with carbon coating with 0. 10mass% of colloidal In this study, colloidal graphite aqueous solution was used as phite suspension, and colloidal graphite was filled between the suspension for carbon coating on the fiber, and carbon layer SiC fibers. The interface between the fiber and the matrix became was formed on Sic fibers by electrophoretic deposition method so weak, and the composite using the fibers coated with 0.50mass% and the sic sic composite was fabricated by sheet stacking method of colloidal graphite suspension could not sustain the applied load and hot-pressing. The effect of the concentration of colloidal effectively and showed a shear fracture behavior, resulting in low graphite on mechanical properties of Sic/sic composite was inves- bending strength and a wide load-crosshead displacement tigated. Bulk density and open porosity of the composites fabri- wer maximum fracture load. From these results. it cated in this study were nearly the same, and these values were that the carbon coating on the fibers was suce independent of the concentration of colloidal graphite suspension. formed by the electrophoretic deposition using colloidal Bending strength gradually decreased with an increase in the
SEM micrographs of the fracture surface of the composites observed from the tensile surface after bending test were shown in Fig. 3. The composite using SiC fibers coated with 0.05mass% of colloidal graphite suspension exhibited short fiber pullout, and fracture surface was almost flat. In the case of the composite using SiC fibers coated with 0.10mass% of colloidal graphite suspension, large fiber pullout was observed. The fracture surface of the composite using SiC fibers coated with 0.50mass% of colloidal graphite suspension was stepwise and showed large fiber pullout. In order to investigate the effect of carbon coating on the SiC fi- ber on bending strength and fracture behavior of the composite, the carbon coating of SiC fiber after electrophoretic deposition was observed by SEM. SEM micrographs of the surface of SiC fibers coated with colloidal graphite suspension by electrophoretic deposition method are shown in Fig. 4. Carbon existed sparsely on the surface of SiC fiber coated with 0.05mass% of colloidal graphite suspension, i.e., carbon was coated non-uniformly on the fiber. It is indicated that the interface between the fiber and the matrix was not uniform and fiber pullout did not occur easily during fracture. As a result, the composite using SiC fibers coated with 0.05mass% of colloidal graphite suspension showed higher bending strength than the composites using SiC fibers coated with 0.10mass% and 0.50mass% of colloidal graphite suspension because the interface between the fiber and the matrix did not act effectively and showed higher friction during fracture. Furthermore, the difficulty in fiber pullout during fracture caused a stepwise fracture behavior and almost flat fracture surface with short fiber pullout. In the case of coating with 0.10mass% of colloidal graphite suspension, relatively uniform carbon coating on the fiber was observed. In consideration of fracture behavior and fracture surface of the composite, it seemed that the optimal interface between the fi- ber and the matrix was obtained by the electrophoretic deposition under this condition. In the case of coating with 0.50mass% of colloidal graphite suspension, carbon layer on the SiC fiber was so thick compared with carbon coating with 0.10mass% of colloidal graphite suspension, and colloidal graphite was filled between SiC fibers. The interface between the fiber and the matrix became so weak, and the composite using the fibers coated with 0.50mass% of colloidal graphite suspension could not sustain the applied load effectively and showed a shear fracture behavior, resulting in low bending strength and a wide load-crosshead displacement curve with lower maximum fracture load. From these results, it was concluded that the carbon coating on the fibers was successfully formed by the electrophoretic deposition using colloidal graphite suspension, and the optimal concentration of colloidal graphite suspension for relatively uniform carbon coating on the fibers was 0.10mass% in this study. 4. Summary In this study, colloidal graphite aqueous solution was used as the suspension for carbon coating on the fiber, and carbon layer was formed on SiC fibers by electrophoretic deposition method, and the SiC/SiC composite was fabricated by sheet stacking method and hot-pressing. The effect of the concentration of colloidal graphite on mechanical properties of SiC/SiC composite was investigated. Bulk density and open porosity of the composites fabricated in this study were nearly the same, and these values were independent of the concentration of colloidal graphite suspension. Bending strength gradually decreased with an increase in the Fig. 3. SEM micrographs of the fracture surface of SiC/SiC composites using SiC fibers coated with various concentration of colloidal graphite suspension observed from the tensile surface after bending test. The concentration of colloidal graphite suspension was (a) 0.05, (b) 0.10 and (c) 0.50mass%. Fig. 2. The typical load-displacement curves of SiC/SiC composites using SiC fibers coated with various concentration of colloidal graphite suspension in bending test at room temperature. The concentration of colloidal graphite suspension was (a) 0.05, (b) 0.10 and (c) 0.50mass%. K. Yoshida et al. / Journal of Nuclear Materials 386–388 (2009) 643–646 645
46 K Yoshida et al. /Journal of Nuclear Materials 386-388 (2009)643-646 concentration of colloidal graphite suspension. In the case of coat- ng with 0. 10mass% of colloidal graphite suspension on SiC fibers relatively uniform carbon coating on the fibers was observed and large fiber pullout occurred effectively during fracture. From the results, it was found that the carbon coating on SiC fibers was suc- cessfully formed by the electrophoretic deposition method using colloidal graphite suspension, and 0. 10mass% of colloidal graphite suspension was optimal for the formation of relatively uniform carbon coating he fiber by the electrophoretic depositi method Acknowledgements 20um Research(No. 17656219)from Japan Society for the Promotion of b Science and The 21st Century COE Program"Innovative Nuclear Energy Systems for Sustainable Development of the world References G.R. Hopkins, R. Price, Nucl Eng Des /Fus. 2(1985)111. R H. Jones, C.H. Henager Jr, G W. Hollenberg, Nucl. Mater. 191-194 (1992) [4]P Fenici, H.W. Scholz, J Nucl. Mater. 212-215(1994)60 [5] H.W. Scholz, M. Zucchetti, K. Casteleyn, C. Adelhelm. ]. Nucl. Mater. 212-215 35H2158320025 le, J Lazzaro, C.w. Lee. J Am Ceram Soc. 66(1983)529. 20u [9]R J Proce, Nucl. Technol. 35(1977)320 11 T Suzuki, T. Yano, T Mor, H Miyazaki, T Iseki, Fus. Technol. 27(1995)314 c [12]S Ueda, S. Nishino, Y. Seki, R Kurihara, J Adachi, S Yamazaki, ] Nucl Mater [131S Sharafat, C.P. C Wong, EE Reis, the ARIES Team, Fus. Technol. 19(1991)901. [14] F Najmabadi, R.W. Conn, the ARIES Team, Proceeding of 14th Internation onference on Plasma Physics and Controlled Nuclear Fusion Research(1992) di, M.S. Tillack, A.R. S.C. Jardin, R.L. Miller, L.M. waganer, of the 14 th Topical Meeting on the 16l 」P Bonal, A. Caso, G. Le Marois, N.B. Morley, J.F. Salavy, Fus. Eng [17] K Yoshida, Budiyanto, M. Imai, T Yano, Nucl Mater. 258-263(1998)1960. [18]K Yoshida, M. Imai, T. Yano, Compos. Sci. Technol. 61(2001)1323 are and Complexity 1(2003)1 [21]K Yo K Hashimoto, Y Toda, T. Yano, Key. Eng 20um Mater.352(2007)7 Fig. 4. SEM micrographs of the SiC fibers coated with various concentration of colloidal graphite suspension by electrophoretic deposition method. The concen- tration of colloidal graphite suspension was(a)0.05,(b)0.10 and (c)0.50mass%
concentration of colloidal graphite suspension. In the case of coating with 0.10mass% of colloidal graphite suspension on SiC fibers, relatively uniform carbon coating on the fibers was observed and large fiber pullout occurred effectively during fracture. From the results, it was found that the carbon coating on SiC fibers was successfully formed by the electrophoretic deposition method using colloidal graphite suspension, and 0.10mass% of colloidal graphite suspension was optimal for the formation of relatively uniform carbon coating on the fiber by the electrophoretic deposition method. Acknowledgements This work was partly supported by Grant-in-Aid for Exploratory Research (No. 17656219) from Japan Society for the Promotion of Science and The 21st Century COE Program ‘‘Innovative Nuclear Energy Systems for Sustainable Development of the World. References [1] G.R. Hopkins, R.J. Price, Nucl. Eng. Des./Fus. 2 (1985) 111. [2] R.H. Jones, C.H. Henager Jr., G.W. Hollenberg, J. Nucl. Mater. 191–194 (1992) 75. [3] L.L. Snead, S.J. Zinkle, D. Steiner, J. Nucl. Mater. 191–194 (1992) 560. [4] P. Fenici, H.W. Scholz, J. Nucl. Mater. 212–215 (1994) 60. [5] H.W. Scholz, M. Zucchetti, K. Casteleyn, C. Adelhelm, J. Nucl. Mater. 212–215 (1994) 655. [6] L.L. Snead, R.H. Jones, A. Kohyama, P. Fenici, J. Nucl. Mater. 233–237 (1996) 26. [7] S.D. Harrison, J.C. Corelli, J. Nucl. Mater. 122&123 (1984) 833. [8] J.C. Corelli, J. Hoole, J. Lazzaro, C.W. Lee, J. Am. Ceram. Soc. 66 (1983) 529. [9] R.J. Proce, Nucl. Technol. 35 (1977) 320. [10] C.H. Wu, J.P. Bonal, B. Kryger, J. Nucl. Mater. 208 (1994) 1. [11] T. Suzuki, T. Yano, T. Mori, H. Miyazaki, T. Iseki, Fus. Technol. 27 (1995) 314. [12] S. Ueda, S. Nishino, Y. Seki, R. Kuriharaq, J. Adachi, S. Yamazaki, J. Nucl. Mater. 258–263 (1998) 314. [13] S. Sharafat, C.P.C. Wong, E.E. Reis, the ARIES Team, Fus. Technol. 19 (1991) 901. [14] F. Najmabadi, R.W. Conn, the ARIES Team, Proceeding of 14th International Conference on Plasma Physics and Controlled Nuclear Fusion Research (1992) 295. [15] F. Najmabadi, M.S. Tillack, A.R. Raffray, S.C. Jardin, R.L. Miller, L.M. Waganer, the ARIES Team, Program and Abstracts of the 14 th Topical Meeting on the Technology of Fusion energy (2000) 164. [16] L. Giancarli, J.P. Bonal, A. Caso, G. Le Marois, N.B. Morley, J.F. Salavy, Fus. Eng. Des. 41 (1998) 165. [17] K. Yoshida, Budiyanto, M. Imai, T. Yano, J. Nucl. Mater. 258–263 (1998) 1960. [18] K. Yoshida, M. Imai, T. Yano, Compos. Sci. Technol. 61 (2001) 1323. [19] K. Yoshida, M. Imai, T. Yano, J. Ceram. Soc. Jpn. 10 (2001) 863. [20] T. Yano, K. Yoshida, Strength, Fracture and Complexity 1 (2003) 157. [21] K. Yoshida, H. Matsumoto, M. Imai, K. Hashimoto, Y. Toda, T. Yano, Key. Eng. Mater. 352 (2007) 77. Fig. 4. SEM micrographs of the SiC fibers coated with various concentration of colloidal graphite suspension by electrophoretic deposition method. The concentration of colloidal graphite suspension was (a) 0.05, (b) 0.10 and (c) 0.50mass%. 646 K. Yoshida et al. / Journal of Nuclear Materials 386–388 (2009) 643–646