Hostname: page-component-586b7cd67f-vdxz6 Total loading time: 0 Render date: 2024-11-25T17:39:40.059Z Has data issue: false hasContentIssue false
  • English
  • Français

Microstructure/Processing Relationships in High-Energy High-Rate Consolidated Powder Composites of Nb-Stabilized Ti3Al + TiAl

Published online by Cambridge University Press:  26 February 2011

C. Persad ,
B.-H. Lee ,
C.-J. Hou ,
Z. Eliezer  and
H. L. Marcus
C. Persad
Affiliation:
Center for Materials Science and Engineering, The University of Texas at Austin, Austin, Texas 78712.
B.-H. Lee
Affiliation:
Center for Materials Science and Engineering, The University of Texas at Austin, Austin, Texas 78712.
C.-J. Hou
Affiliation:
Center for Materials Science and Engineering, The University of Texas at Austin, Austin, Texas 78712.
Z. Eliezer
Affiliation:
Center for Materials Science and Engineering, The University of Texas at Austin, Austin, Texas 78712.
H. L. Marcus
Affiliation:
Center for Materials Science and Engineering, The University of Texas at Austin, Austin, Texas 78712.
Get access

Abstract

A new approach to powder processing is employed in forming titanium aluminide composites. The processing consists of internal heating of a customized powder blend by a fast electrical discharge of a homopolar generator. The high-energy high-rate “1MJ in 1s” pulse permits rapid heating of an electrically conducting powder mixture in a cold wall die. This short time at temperature approach offers the opportunity to control phase transformations and the degree of microstructural coarsening not readily possible with standard powder processing approaches. This paper describes the consolidation results of titanium aluminide-based powder composite materials. The focus of this study was the definition of microstructure/processing relationships for each of the composite constituents, first as monoliths and then in composite forms. Non-equilibrium phases present in rapidly solidified TiAl powders are transformed to metastable intermediates en route to the equilibrium gamma phase. The initial single phase beta in Nb-stabilized Ti3Al is transformed to alpha two with an intermediate beta two phase. In composite blends of TiAl powders mixed with Nb-stabilized Ti3Al powders a 10 μm thick interfacial layer is formed on the dispersed TiAl. Limited control of post-pulse heat extraction prevents full retention of the rapidly solidified powder microstructures.

Type
Research Article
Information
MRS Online Proceedings Library (OPL) , Volume 133: Symposium H – High-Temperature Ordered Intermetallic Alloys III , 1988 , 717
Copyright
Copyright © Materials Research Society 1989

Access options

Get access to the full version of this content by using one of the access options below. (Log in options will check for institutional or personal access. Content may require purchase if you do not have access.)

References

REFERENCES

[1] Murray, Joanne L., Met. Trans. 19A, 243 (1988).CrossRefGoogle Scholar
[2] Whang, S. H., Li, Z. X., and Vujic, D. in High-Temperature Ordered Intermetallic Alloys II, edited by Stoloff, N. S., Koch, C. C., Liu, C. T., and Izumi, O. (Mater. Res. Soc. Proc. 81, Pittsburgh, PA 1987) pp. 151–156.Google Scholar
[3] Huang, S. C., Hall, E. L., and Gigliotti, M. F. X. in High-Temperature Ordered Intermetallic Alloys II, op. cit., pp. 481–486.Google Scholar
[4] Strychor, R., Williams, J. C., and Soffa, W. A., Met. Trans. 19A, 225 (1988).Google Scholar
[5] Lipsitt, H. A., in High-Temperature Ordered Intermetallic Alloys, edited by Koch, C. C. et. al., ( Mater. Res. Soc. Proc. 39, Pittsburgh, PA 1985) pp. 351–364.Google Scholar
[6] Lipsitt, H. A., in Advanced High-Temperature Alloys: Processing and Properties, edited by Allen, S. M. et al.(ASM, Ohio, 1986) pp. 157–164.Google Scholar
[7] Fine, M. E., Bourell, D. L., Eliezer, Z., Persad, C. and Marcus, H. L., Scripta Metallurgica, 22, 907 (1986).CrossRefGoogle Scholar
[8] Williams, J. C., in Precipitation Processes in Solids, Russell, K. C. and Aaronson, H. I., eds., (TMS-AIME, Warrendale, 1978) p. 191.Google Scholar
[9] Marcus, H. L., Bourell, D. L., Eliezer, Z., Persad, C. and Weldon, W. F., Journal of Metals, 39, 6 (December 1987).Google Scholar
[10] Elkabir, G., Rabenberg, L., Persad, C. and Marcus, H.L., Scripta Met. 20, 1411 (1986).Google Scholar
[11] Ervin, D. R., Bourell, D., Persad, C., Rabenberg, L., J. Mat. Sci. Eng. A102, 25 (1988).CrossRefGoogle Scholar
[12] Price, C.E. in Metals Handbook. 9th. edition. V. 9. Metallography and Microstructures (ASM, Metals Park, OH, 1985) p. 151.Google Scholar
[13] Rosenberg, H. W. and Nix, W. D., Met. Trans. 1 2962 (1970).CrossRefGoogle Scholar
[14] Bridenbaugh, P. R., Billman, F. R., Cebulal, W. S., and Hildeman, G. J., in Advanced High-Temperature Alloys: Processing and Properties, op. cit., pp. 53–64.Google Scholar
[15] Blackburn, M. J. and Smith, M. P., U. S. Patent No. 4 292 077 ( 29 September 1981).Google Scholar
[16] Hou, C. -J. et al., presented at the 1988 TMS/AIME Fall Meeting, Chicago, IL, 1988.Google Scholar
[17] Jackson, A. G., Teal, K. and Froes, F. H. in High-Temperature Ordered Intermetallic Alloys II op. cit., pp. 143–149.Google Scholar
[18] Banerjee, D., Gogia, A. K., Nandi, T. K. and Joshi, V. A, Acta Metall. 36, 871 (1988).Google Scholar