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WELDING RESEARCH OCTOBER 2002-S210 350°C (662°F) for 100 days (Fig. 14A) had the same hillock features as did the f

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Content	WELDING RESEARCH OCTOBER 2002-S210 350°C (662°F) for 100 days (Fig. 14A) had the same hillock features as did the frac- ture surface of the as-fabricated (Fig. 9B). Also, the aging treatment caused small peaks and valleys to appear on the fracture surface. The aging treatment at 575°C (1067°F) for 200 days caused the hillock structures to largely disappear; however, the fine peak and valley morphology re- mained on the fracture surfaces. Shown in Fig. 15 is the optical micrograph of the cross section of a tested bend bar that had been aged at 575°C (1067°F) for 200 days. The fracture path lay at the Thermo- Span™/Ag-Cu-Ti interface (as was simi- larly observed in the as-fabricated case). More specifically, however, the fracture path was observed to move between the reaction layer/Thermo-Span™ interface and the reaction layer/braze alloy inter- face. The scale of these fracture path jumps appeared to be commensurate with the fine scale peaks and valleys observed on the fracture surfaces. The bend strength data aged Inconel™ 718/Ag-Cu-Ti specimens appear in Fig. 13B. As was the case with the Thermo- Span™/Ag-Cu-Ti couples, the aging treat- ments did not cause a significant change to the strength values. Similarly, the fracture paths were not changed from their base metal/filler metal interface. In summary, the four-point bend strengths for both the Thermo-Span™ and Inconel™ 718 braze joints made with the Ag-Cu-Ti filler metal were not signifi- cantly affected by the aging treatments. The fracture paths remained located gen- erally at the base metal/filler metal inter- face with only some minor differences being observed in the finer details of the fracture surfaces as a consequence of the aging treatments. Summary 1) The effects of aging were examined for brazed joints made between the 63.3Ag-35.1Cu-1.6Ti filler metal and Thermo-Span™ and Inconel™ 718 base metals. 2) Excellent wetting and spreading was exhibited by the Ag-Cu-Ti filler metal on both base metals as determined by contact angle measurements. 3) The as-fabricated Thermo- Span™/Ag-Cu-Ti brazed joints exhibited two sublayers at the base metal/filler metal interface. Each sublayer contained (Fe, Ni, Co, Cu)2(Nb, Ti, Si, Cr) and silver in a volume ratio of 9:1. The two sublayers were separated by a Ag-rich zone. Aging reduced the reaction zone to one sublayer having a composition of (Fe, Ni, Co, Cu)2(Nb, Ti, Si, Cr). The thickness of this layer was less than the total reaction zone of the as-fabricated specimen. 4) The interface reaction zone in the as-fabricated Inconel™ 718/Ag-Cu-Ti specimens contained two sublayers. Sub- layer No. 1, located next to the base metal, had the composition of (Fe,Ni,Cu)3(Ti,Cr,Nb,Mo)2. Sublayer No. 2, located next to the filler metal field, had the composition of (Fe,Ni,Cu)2(Ti,Cr,Nb,Mo). The composition of sublayer No. 1 remained unchanged after aging. The composition of sublayer No. 2 shifted to primarily (Fe,Ni,Cu)7(Ti,Cr,Nb,Mo)3, but with some localized variations along the interface. Aging caused growth of the overall interface re- action layer. 5) The four-point bend strengths ob- served with the as-fabricated Thermo- Span™/Ag-Cu-Ti and Inconel™ 718/Ag- Cu-Ti specimens were not significantly changed after each of the aging treat- ments. The fracture path remained lo- cated at the base metal/filler metal inter- face for as-fabricated as well as for aged test specimens. Acknowledgments The authors wish to thank A. Kilgo, who performed the metallographic sample preparation; P. Hlava, who performed the EMPA; and B. Ritchey for the SEM mi- crographs. The authors would also like to thank C. Robino for his very thorough re- view of the manuscript. Sandia is a multi- program laboratory operated by Sandia Corporation, a Lockheed Martin Com- pany, for the United States Dept. of Energy under contract DE-AC04- 94AL85000. References 1. Mangin, C., Neely, J., and Clark, J. 1993. The potential for advanced ceramics in auto- motive engine applications. Journal of Metals (6): 23–27. 2. DeLuca, M., and Swain, J. 1987. An ad- vanced ceramic-to-metal joining process. Ce- ramic Eng. Sci. Proc.8(7-8): 602–610. 3. Santella, M. 1993. Joining of ceramics for heat engine applications. Ceramic Tech. Pro- ject-Semiannual Prog. Rep., ORNL/TM-12428, pp. 167–180, Oak Ridge National Laboratory, Oak Ridge, Tenn. 4. Levy, A. 1991. Thermal residual stresses in ceramic-to-metal brazed joints. J. Am. Ce- ramic Soc.74(9): 2141–2147. 5. Moorhead, A., and Hyoun, K. 1992. Join- ing oxide ceramics. Engineered Materials Hand- book,Vol. 4, Ceramics and Glasses, pp. 511–522. Materials Park, Ohio: ASM International. 6. Santella, M. 1993. Ceramic-metal joining ceramic technology project, Semiannual progress report, 10/92−3/93: pp. 167–180. Oak Ridge, Tenn: National Laboratory. 7. Kovar™, Invar 36™, and Alloy 42™ are registered trademarks of Carpenter Technology Corp., Reading, Pa. 8. Harner, L. 1994. Selecting controlled ex- pansion alloys. Advanced Materials and ProcessesOctober: 19–22. 9. Bex, W. 1989. Metallurgical study of su- peralloy brazing alloys. Proc. Propulsion and Energetics Panel 72nd Specialists’ Meeting, Bath, U.K., pp. 27–12. 10. Sasabe, K. 1991. Effect of joint clearance on fatigue strength of brazed joint. Trans. Nat. Res. Inst. For Metals33(1): 36–41. 11. Dicus, D., and Buckley, J. 1972. The ef- fects of high-temperature brazing and thermal cycling on the mechanical properties of Hastel- loy X. NASA Langley Research Center Report, L-8376, pp. 1–21. 12. Shimoo, T., Kobayashi, Y., and Oka- mura, K. 1992. Kinetics of reaction of Si3N4with Ni. Journal of the Ceramic Soc. of Japan, In- ternational Edition 100, pp. 801–806. 13. Naka, M. 1992. Controlling of ceramic- metal interfacial structure using molten metals. Trans. Weld. Res. Inst.21: 1–7. 14. Boadi, J., Yano, T., and Iseki, T. 1987. Brazing of pressureless-sintered SiC using Ag- Cu-Ti alloy. Journal of Material. Sci.22: 2431–2434. 15. Bang, K., and Liu, S. 1994. Interfacial re- action between alumina and Cu-Ti filler metal during reactive metal brazing. Welding Journal 73(3): 54-s to 60-s. 16. Kodentsov, A., Kivilahti, J., and Loo, F. 1993. Interfaces in Si3Ni4/Ni-Cr alloy joints.Ce- ramic Trans. 35: 1–10. 17. Beraud, C., Courbiere, M., Esnour, C., Juve, D., and Treheux, D. 1989. Study of cop- per-alumina bonding. J. Mater. Sci.24: 4545–4554. 18. Allen, R., and Borbidge, W. 1983. Solid state metal-ceramic bonding of platinum to alu- mina. J. Mater. Sci. 18: 2835–2843. 19. Thermo-Span™ is a registered trade- mark of Carpenter Technologies Corp., Read- ing, Pa. 20. Inconel™ is a registered trademark of Huntington Alloys, Huntington, W.Va. 21. Cusil™ is a registered trademark of WESGO Products. 22. Binary Alloy Phase Diagrams,Vol. 2, 1986. Ed. by T. Massalski, pp. 764, 783, 1086. Materials Park, Ohio: ASM International. 23. ibid. pp. 760, 916, and 942. 24. ibid. p. 971. 25. ibid. pp. 780, 1084, 1682, and 1704.
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