Damping properties of Ti50Ni50−xCux alloys utilizing martensitic transformation
Introduction
The vibration problem is a serious one in the modern world e.g. in the aerospace, transportation, and manufacturing industries as well as in environmental engineering. Thus various damping materials are being developed. Among many damping mechanisms, the one utilizing the martensitic/displacive transformation in shape memory alloys is useful, since the martensitic transformation introduces a high density of mobile twins in martensites [1], and mobile phase boundaries between the parent phase and martensite, which contribute to the internal friction. Among many shape memory alloys, Ti–Ni alloys are attracting much attention from researchers, since these alloys provide high damping as well as high strength, which is crucial for structural materials. The internal friction in Ti–Ni alloys was studied by many researchers [2], [3], [4], [5], [6], [7], and the general trend, with some exceptions (which depend upon thermomechanical treatments), is that IF consists of two peaks: a sharp transient peak due to the martensitic transformation and a very broad peak so-called ‘relaxation type’, whose peak usually situated at around 200 K [8], [9]. The relaxation type peak is usually considered to be due to the twin boundary movement under stress. In practical applications this relaxation type IF is more important than the transient IF due to the martensitic transformation, since the IF in the former is stable at constant temperature, while that in the latter decreases rapidly when the temperature is held at a constant temperature, as Delorme’s theory [10] predicts. Although Ti–Ni alloys are good damping materials, one of the shortcomings is that high damping characteristics are obtained at rather low temperatures (i.e. below room temperatures) as the peak temperature of the broad peak of 200 K indicates. To resolve the problem and to obtain higher damping characteristics, we undertook the present work.
In binary Ti–Ni alloys quenched specimens transform from B2 parent to B19′ (monoclinic) martensite, while Ni-rich specimens, which are aged at proper temperatures (say 673–873 K), transform to R-phase (trigonal) followed by the subsequent transformation to B19′ martensite [11]. The Ni-rich aged specimens usually show lower transformation temperatures, thus are not useful in increasing transformation temperature. In the present investigation we investigated Ti50Ni50−xCux (8≦x≦20) alloys for two reasons. Firstly the transformation mode changes into B2–B19 (orthorhombic) rather than B2–B19′, which may be followed further by B19–B19′ transformation upon further cooling, depending on composition, when the Cu content is increased to higher than x=7.5 [12]. Secondly the first transformation temperature (i.e. that for B2–B19) increases gradually with increasing Cu content [12]. There are some pioneering works [13], [14] on internal friction of Ti50Ni40Cu10 alloy already, which will be referred to in Results and discussions, but in the present work we will investigate much wider composition ranges, as indicated in the above, to understand the damping characteristics of the alloy system.
Section snippets
Experimental
The nominal compositions of the alloys used were Ti50Ni50−xCux (x=8, 10, 12, 16, 20). These alloy ingots were prepared by a high frequency vacuum induction furnace with a carbon crucible. Then the fabrication processes were divided into two depending upon composition. The alloys with x=8 and 10 were made by hot-extrusion, hot-rolling, followed by the subsequent cold-drawing to wires with a final diameter of 1.5 mm, while those with x>10 were made to slabs by hot-extrusion, and then spark-cut
Results and discussion
The results of internal friction and f2 (f=frequency) measurements for the above alloys are shown in Fig. 1, Fig. 2, Fig. 3, Fig. 4, Fig. 5. Since f2 is proportional to the rigidity of a specimen, we can recognize the temperature dependence of f2 as that of rigidity of the specimens. In the figures we find common features described below among Ti50Ni50−xCux alloys. i.e. the IF spectrum consists of a broad peak situated at around 250 K and a small peak (or a shoulder) at the higher temperature
Conclusions
By studying the internal friction of Ti50Ni50−xCux (x=8, 10, 12, 16, 20) alloys by the inverted torsion pendulum method, the following results were obtained.
- 1.
Extraordinarily large IF and the softening in rigidity were observed for the whole composition range examined. The peak temperature of the broad peak is located at around 250 K irrespective of composition, which is higher than the relaxation type peak in Ti–Ni binary alloys located at around 200 K. The large broad peak at 250 K is
Acknowledgements
The authors are grateful to Drs. Y. Nakata, X. Ren and Ya Xu for useful discussions. The present work was supported by The High Damping Material Project of Research for the Future (RFTF) of Japan Society for Promotion of Science (JSPS).
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