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Effect of Superelastically Deforming NiTi Surface Microalloys on Fatigue Crack Nucleation in Copper.

Published online by Cambridge University Press:  25 February 2011

D. S. Grummon ,
S. Nam  and
L. Chang
D. S. Grummon
Affiliation:
Department of Metallurgy, Mechanics and Materials Science, Michigan State University, East Lansing, MI 48824
S. Nam
Affiliation:
Department of Metallurgy, Mechanics and Materials Science, Michigan State University, East Lansing, MI 48824
L. Chang
Affiliation:
Department of Metallurgy, Mechanics and Materials Science, Michigan State University, East Lansing, MI 48824
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Abstract

Alloys based on near-equiatomic NiTi are capable of thermoelastic martensite transformations which give rise to shape memory and superelasticity (pseudoplasticity) effects. In particular, at temperatures above Ms and Af but below Md, NiTi alloys can deform by mechanisms of stressinduced martensite transformation and may display large anelastic strains which involve little or no deformation by slip. Under these conditions, the strain-controlled fatigue resistance of NiTi alloys may be exceptionally high [1]. In contrast, fcc metals like copper will, during strain controlled fatigue, eventuate severe plastic strain localization in the form of persistent slip bands (PSBs), whose behavior at free surfaces is intimately associated with fatigue crack initiation [2]. It is well known that fatigue crack initiation in fcc metals can be delayed by modifying surfacebreaking PSB structure or environment [3,4]. However, any attempt to strengthen the surface region in order to impede surface expression of persistent slip bands must contend with the large subsurface strain localizations enforced by the PSBs, which subject the film to strain cycling at roughly the characteristic PSB shear strain amplitude. Thermoelastic nickel-titanium alloys, capable of pseudoplastic straining, may be uniquely suited to the role of surface protection in situations where fatigue crack initiation is associated with PSB interaction with the external environment. In the present work, thin surface microalloys of NiTi, produced by ion sputtering, have been applied to polycrystalline copper fatigue specimens that were subsequently subjected to both monotonic loading, and fatigue under plastic strain control to produce mature PSB structures in the bulk material. Optical and scanning electron microscopy studies are described which assess the effect of the NiTi surface microalloy on the behavior of PSBs in the near surface region, and the attendant effect of the films on surface behavior of persistent slip bands. Although the results are incomplete with respect to the effects of the film on fatigue crack initiation, it has been shown for the first time that martensite transformation can be stress-induced (at temperatures above Ms) in a thin NiTi film on a plastically deforming substrate. This finding augurs well for the potential of such films to effectively suppress slip band penetration during low cycle fatigue.

Type
Research Article
Information
MRS Online Proceedings Library (OPL) , Volume 246: Symposium M – Shape-Memory Materials and Phenomena--Fundamental Aspects and Applications , 1991 , 259
Copyright
Copyright © Materials Research Society 1992

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References

1. Melton, K. N. and Mercier, D., Acta. Met. 27, PP 137–144 (1979).CrossRefGoogle Scholar
2. Neumann, P. and Tonnessen, A., in Fatigue 87. Ritchie, D. and Starke, E. A., Eds., Proc. 3rd Inl. Conf. on Fatigue and Fatigue Thresholds, Charlottesville, Va., June 1987.Google Scholar
3 Greenfield, I.T. and Purohit, A., in Surface Effects in Cp stal Plasticiy, Adv. Study In on Surface Effects in Crystal Plasticity, Hohegeiss, Ger., Latanison, R. M. and Fouriep, J. T. Eds. pp. 609–624 (1977).Google Scholar
4. Grummon, D. S. and Jones, J.W., Metall. Trans 19A, pp 2775–2788 (1988).CrossRefGoogle Scholar
5. Thompson, N., Wadsworth, N. J. and Louat, N., Phil. Mag. 1, p. 113 (1956).CrossRefGoogle Scholar
6. morrison, D.J., Jones, J.W., Alexander, D.E. and Was, G. S. Metal. Trans 22A, p1633–1645 (1991).CrossRefGoogle Scholar
7. Meyers, C.A. and Grummon, D. S., Mater. Sci. Eng., A130, pp. 127–138 (1990).CrossRefGoogle Scholar
8. Buehler, W. J. and Wang, F. E., Ocean Eng. 1, pp 105–120 (1968).CrossRefGoogle Scholar
9. Tadaki, T. and Wayman, C. M., Scripta Met. 14, pp 911–914 (1980).CrossRefGoogle Scholar
10. Kosmac, T., Swain, M. V. and Claussen, N., Mater. Sci. Eng. 71, pp57–64 (1985).CrossRefGoogle Scholar
11. Melton, K. N. and Mercier, O., in Strength of Metals and Alloys, Haasen, P., ed., V.2, pp 1243–1248 (1979).CrossRefGoogle Scholar
12. Melton, K. N. and Mercier, O., Met. Trans. 9A, pp1487–1488 (1978).CrossRefGoogle Scholar
13. Laird, C., 1975 in Treatise on Materials and Technology Arsenault, R. J., Ed. Academic Press, San Fransisco, pp 101–162 (1975).Google Scholar