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Effect of Sn addition on stress hysteresis and superelastic properties of a Ti-15Nb-3Mo alloy

Effect of Sn addition on stress hysteresis and superelastic properties of a Ti-15Nb-3Mo alloy
Effect of Sn addition on stress hysteresis and superelastic properties of a Ti-15Nb-3Mo alloy

Accepted Manuscript

Effect of Sn addition on stress hysteresis and superelastic properties of a

Ti-15Nb-3Mo alloy

Muhammad Farzik Ijaz, Hee Young Kim, Hideki Hosoda, Shuichi Miyazaki

PII:S1359-6462(13)00505-8

DOI:https://www.doczj.com/doc/6f8206353.html,/10.1016/j.scriptamat.2013.10.007

Reference:SMM 10081

To appear in:Scripta Materialia

Received Date:12 September 2013

Revised Date:8 October 2013

Accepted Date:10 October 2013

Please cite this article as: M.F. Ijaz, H.Y. Kim, H. Hosoda, S. Miyazaki, Effect of Sn addition on stress hysteresis and superelastic properties of a Ti-15Nb-3Mo alloy, Scripta Materialia(2013), doi: https://www.doczj.com/doc/6f8206353.html,/10.1016/ j.scriptamat.2013.10.007

This is a PDF file of an unedited manuscript that has been accepted for publication. As a service to our customers we are providing this early version of the manuscript. The manuscript will undergo copyediting, typesetting, and review of the resulting proof before it is published in its final form. Please note that during the production process errors may be discovered which could affect the content, and all legal disclaimers that apply to the journal pertain.

Effect of Sn addition on stress hysteresis and superelastic

properties of a Ti-15Nb-3Mo alloy

Muhammad Farzik Ijaz a , Hee Young Kim a,*, Hideki Hosoda b and Shuichi Miyazaki a,c,** a Division of Materials Science, University of Tsukuba, Tsukuba, Ibaraki 305-8573,

Japan b Precision and Intelligence Laboratory, Tokyo Institute of Technology, Yokohama

226-8503, Japan

c Center of Excellence for Advance

d Materials Research, King Abdulaziz University,

PO Box 80203, Jeddah 21589, Saudi Arabia

* Corresponding author. Tel./Fax: +81 29 853 6942.

**

Corresponding author. Tel./Fax: +81 29 853 5283. E-mail addresses: heeykim@ims.tsukuba.ac.jp (H. Y. Kim),

miyazaki@ims.tsukuba.ac.jp (S. Miyazaki).

The effects of Sn content on stress hysteresis and superelastic properties of Ti-15Nb-3Mo-(0-1.5)Sn were investigated. The stress hysteresis decreased with increasing Sn content due to the suppression of athermal omega phase formation. The addition of Sn was also very effective for increasing superelastic recovery strain. Due

to a two-fold role of Sn, i.e. on the martensitic transformation temperature and omega phase, the stress for inducing martensitic transformation decreased with increasing Sn content up to 1at.%, then increased by further addition.

Keywords: Titanium alloys; Shape memory alloys; Superelasticity

Ti-Ni alloys have been successfully utilized in various biomedical devices due to their exceptional superelastic properties. The major biomedical applications of Ti-Ni alloys have been found in devices such as stents, guide wires and dental arch wires [1]. However, despite their excellent superelastic performance and successful safe usage for medical applications, there are still concerns over the high concentration of Ni in various Ti-Ni-based superelastic alloys. Therefore efforts have been devoted to develop new classes of Ni-free Ti-based superelastic alloys [2-8]. Among them, Ti-Nb-based alloys have been able to get significant attention [7-13]. Superelasticity in Ti-Nb-based alloys is attributed to the reversible stress-induced martensitic transformation between parent βphase (bcc) and martensite α" phase (orthorhombic structure) [14, 15]. Superelastic recovery strain is primarily dependent on the transformation strain which is determined by the crystal structures of parent phase and martensite phase. Recently our group reported that the addition of Mo to Ti-Nb alloys is very effective to increase superelastic recovery strain due to the solid solution strengthening effect of Mo and the increase in transformation strain [16]. However, excess addition of Mo for the replacement of Nb in Ti-Nb-Mo alloy system deteriorates superelastic properties mainly due to the formation of a large amount of athermal ω phase [16]. It was also reported that the increase in Mo content significantly increases the stress hysteresis of Ti-Nb-Mo

alloys [17]. A small stress hysteresis is preferable for superelastic alloys to take advantage of a high recovery force. In this study, we show that the addition of Sn is very effective not only to reduce stress hysteresis but also to improve superelastic recovery strain of a Ti-Nb-Mo alloy. The unique Sn content dependence of the critical stress for inducing martensitic transformation in Ti-15Nb-3Mo alloys is analyzed by microstructural observation.

Ti-15Nb-3Mo-(0-1.5)Sn (at.%) (all compositions are hereafter described in atomic per cent) ingots were prepared by arc-melting in an Ar atmosphere. The ingots were homogenized at 1273 K for 7.2 ks followed by cold-rolling up to 98.5% reduction in thickness without intermediate annealing. Specimens for tensile tests, X-ray diffraction (XRD) measurements and transmission electron microscope (TEM) observation were cut from the as-rolled strips using an electric discharge cutting machine. All the specimens were heat-treated at 973 K for 0.6 ks in an Ar filled quartz tube, followed by quenching in water. Superelastic properties were characterized by loading-unloading tensile tests at room temperature (298 K). The dimensions of the tensile specimens were 0.14 mm in thickness and 1.5 mm in width, with a length of 40 mm. Tensile tests were performed using a Shimadzu Autograph 5KN tensile testing machine at a cross-head speed of 2.5 х 10-4 s-1. Both ends of the tensile specimens were fixed with in two chucks so that gage length becomes 20 mm and the strain of the specimens was determined by measuring the distance between the chucks using an extensometer. Constituent phases were investigated using an XRD machine with a Cu Kαradiation source. Microstructural analysis was conducted by TEM, using a JEOL 2010F microscope operated at 200 kV.

Figure 1a shows stress–strain curves of Ti-15Nb-3Mo-(0-1.5)Sn alloys obtained at room temperature. The specimen was elongated until reaching 2.5% strain and then unloaded. All the alloys exhibited superelastic recovery. A single headed arrow points at the critical stress required for inducing martensitic transformation (σβ→α"), whereas a double head arrow points at the stress where the reverse transformation finishes (σα"→β) upon unloading. Stress hysteresis (?σ) was defined as the difference between σβ→α" and σα"→β.

The Sn content dependences of σβ→α" and σα"→βare shown in Figure 1b. So far, it has been reported that Sn decreases M s of Ti-Nb based alloys [18, 19]. Therefore, it is expected that σβ→α"increases with increasing Sn content, since the stress for inducing martensitic transformation at a fixed test temperature increases with decreasing M s of the alloy. However, Figure 1b shows a peculiar Sn content dependence of σβ→α": it decreased by the addition of Sn up to 1 at.%, and then increased by further addition. This implies that the addition of Sn up to 1 at.% raised M s of the Ti-15Nb-3Mo alloy, but further addition caused the decrease of M s. On the other hand, σα"→β exhibited a monotonic increasing tendency with the increase in Sn content as shown in Figure 1b. It is important to note that the addition of Sn causes a significant decrease in ?σof the Ti-15Nb-3Mo alloy. It is apparent that the decreasing trend of ?σ is more pronounced particularly up to 1 at.% Sn addition as shown in Figure 1c.

In order to investigate superelastic properties of the Ti-15Nb-3Mo-(0-1.5)Sn alloys, cyclic loading–unloading tensile tests were carried out and the results are shown

in Figure 2. In the first cycle, the tensile stress was applied until the strain reached 1.5% and then unloaded. The similar measurement was repeated by increasing maximum strain by the interval of 0.5% (such as 1.5 %, 2.0% for each successive cycle of loading) using the same specimen. In order to evaluate superelastic properties, two types of strain, i.e. recovery strain (εr) and remained plastic strain (εp) were measured at each cycle. It is seen that the strain was almost totally recovered upon unloading up to the first cycle for Ti-15Nb-3Mo, up to the third cycle for Ti-15Nb-3Mo-0.5Sn and Ti-15Nb-3Mo-0.75Sn, up to the fourth cycle for Ti-15Nb-3Mo-1Sn and Ti-15Nb-3Mo-1.25Sn, and up to the first cycle for Ti-15Nb-3Mo-1.5Sn, respectively. The magnitudes of maximum recovery strain εr max, σβ→α" and ?σ are listed in Table 1. Interestingly, these properties, i.e. εr max, σβ→α"and ?σshow different Sn content dependences. As mentioned above, with increasing Sn content σβ→α"decreased to minimum at Ti-15Nb-3Mo-1Sn and it was then increased by further addition of Sn. On the other hand, ?σ exhibited a monotonic decreasing tendency with increasing Sn content. The decrease in the stress hysteresis caused the increase in the superelastic recovery strain; εr max increased to a maximum value of 3.7% at Ti-15Nb-3Mo-1.25Sn. However Ti-15Nb-3Mo-1.5Sn exhibited a small recovery strain of 2.1% in spite of its smallest stress hysteresis. It is suggested that the small recovery strain of Ti-15Nb-3Mo-1.5Sn is due to its high σβ→α". A high σβ→α"reduces the difference between the critical stress for permanent plastic deformation and the stress for inducing martensitic transformation, resulting in that the permanent plastic deformation occurs during the martensitic transformation.

In order to discuss the effect of Sn content on superelastic properties, XRD measurement and TEM observation were carried out. Figure 3a shows XRD profiles of the Ti-15Nb-3Mo-(0-1.5)Sn alloys obtained at room temperature. Within the measured 2θ (deg.) range, β phase was identified by four major reflections from (110)β, (200)β, (211)β, and (222)βwhereas ωphase was identified by two major reflections from (001)ω and (002)ω. The reflections from the ω phase are found to be sensitive to the Sn content. It is clearly seen that the Ti-15Nb-3Mo alloy reveals the strongest intensity of the ωphase. The ωphase is suggested to be formed athermally during quenching from the annealing temperature (973 K). The peak intensities of the ω phase gradually became weaker as the Sn content increased. The peaks from the ωphase could not be detected in the XRD profiles of the Ti-15Nb-3Mo-1.25Sn and Ti-15Nb-3Mo-1.5Sn alloys. This implies that the ω phase was suppressed significantly with the increase in Sn content, which is consistent with previous works [20, 21]. The suppression of athermal omega phase (ωath) by the addition of Sn was also confirmed by TEM observation. Figure 3b shows dark-field images and the corresponding selected area diffraction patterns with zone axis of [113]βin the Ti-15Nb-3Mo and Ti-15Nb-3Mo-1Sn alloys. Dark-field images showing the ω phase were formed using the diffraction spot indicated by a white circle in each diffraction pattern. It is seen that the size and volume fraction of the ωath phase were remarkably reduced by the Sn addition.

On the basis of microstructure analysis, the unique Sn content dependences of σβ→α"and stress hysteresis in the Ti-15Nb-3Mo-(0-1.5)Sn alloys can be explained by considering a two-fold role of Sn; the one hand Sn decreases M s of Ti-Nb based alloys, on the other hand it suppresses the ω phase formation. It has been confirmed that the athermal ωphase suppresses the martensitic transformation and increases in σβ→α"of Ti-Nb-Mo alloys [16, 17], implying that the suppression of the athermal ωphase increases M s. Figure 4 illustrates the schematic explanation of the effect of Sn on apparent M s and σβ→α". If we only consider the compositional effect, σβ→α"should increase monotonically with increasing Sn content because the difference between M s and test temperature (RT) increases. However, a large amount of athermal ω phase in the Ti-15Nb-3Mo alloy decreases M s and increases σβ→α"of the alloy. As mentioned above, the volume fraction of athermal ω phase decreases with increasing Sn content, indicating that the decrease in M s due to the ωphase is reduced as the Sn content increases. Consequently the decrease in σβ→α" with increasing Sn content up to 1 at.% in the Ti-15Nb-3Mo-(0-1.5)Sn alloys implies the fact that the effect of Sn on the suppression of athermal ωphase is stronger than the compositional effect which decreases M s. As the Sn content increased the effect of Sn on the suppression of athermal ω phase becomes weaker, hence the compositional effect becomes dominant. This explains why σβ→α" increases with increasing Sn content from 1 at.% to 1.5 at.%.

On the other hand, the monotonic increase in σα"→β with increasing Sn content suggests that the intrinsic compositional effect of Sn is dominant for the reverse transformation. It has been proposed that the athermal ω phase also transforms into the α" phase when the β phase transforms [17, 22]. As a result, according to the current understanding, it is believed that the monotonic change in σα"→β is mainly attributed to the absence of the ωphase in the α" phase while unloading. This explains not only a large stress hysteresis loop in the ternary alloy but also the decrease of stress hysteresis with increasing Sn content.

In conclusion, we are able to reduce the stress hysteresis and increase the superelastic recovery strain of a Ti-Nb-Mo alloy by the addition of Sn. The decrease in the stress hysteresis with increasing Sn content is due to the suppression of the athermal ωphase. The unique Sn content dependence of the critical stress for inducing martensitic transformation in Ti-15Nb-3Mo-(0-1.5)Sn alloys is due to a two-fold role of Sn, i.e. the decrease of M s and the suppression of the athermal ω phase.

Acknowledgments

This work was partially supported by JSPS KAKENHI Grant Number 23360300 and 25289247, MEXT KAKENHI Grant Number 23102503 and 25102704.

References

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List of Figure captions.

Figure 1. (a) Stress-strain curves of Ti-15Nb-3Mo-(0-1.5) Sn alloys, (b) effect of Sn content on σβ→α" and σα"→β and (c) effect of Sn content on stress hysteresis ?σ.

Figure 2. Stress-strain curves obtained by cyclic loading–unloading tensile tests for Ti-15Nb-3Mo-(0-1.5) Sn alloys.

Figure 3. (a) XRD profiles for Ti-15Nb-3Mo-(0-1.5)Sn alloys and (b) dark field images and the corresponding selected area diffraction patterns for Ti-15Nb-3Mo and Ti-15Nb-3Mo-1Sn alloys.

Figure 4. A schematic explanation on the effect of Sn on Ms and σβ→α".

Figure 1.(a) Stress-strain curves of Ti-15Nb-3Mo-(0-1.5) Sn alloys, (b) effect of Sn content on σβ→α" and σα"→β and (c) effect of Sn content on stress hysteresis ?σ.

Figure 2.Stress-strain curves obtained by cyclic loading–unloading tensile tests for Ti-15Nb-3Mo-(0-1.5) Sn

alloys.

alloys and (b) dark field images and the corresponding selected

area diffraction patterns of Ti-15Nb-3Mo and Ti-15Nb-3Mo-1Sn alloys.

and σβ→α".

Table 1.Summary of superelastic properties obtained by cyclic loading-unloading tensile tests of Ti-15Nb-3Mo-(0-1.5)Sn alloys.

Alloy (at.%)

σβ-α″

(MPa)

(MPa)

εr max

(%)

Ti-15Nb-3Mo-0Sn297 253 2.1 Ti-15Nb-3Mo-0.5Sn259 212 3.1 Ti-15Nb-3Mo-0.75Sn252 172 3.2 Ti-15Nb-3Mo-1Sn212 123 3.3 Ti-15Nb-3Mo-1.25Sn271 121 3.7 Ti-15Nb-3Mo-1.5Sn344 78 2.1

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算法模板【最后更新2014-05】

算法模板 网络122 王硕

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1.1矩阵 #include #include using namespace std; const int MAXN=100; const int MAXM=100; struct Matrix { int n,m; int a[MAXN][MAXM]; void clear() { m=n=0; memset(a,0,sizeof(a)); } Matrix operator +(const Matrix &b) const { Matrix tmp; tmp.n=n; tmp.m=m; for(int i=0;i

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string ADD_INT(string str1, string str2) { string MINUS_INT(string str1, string str2); int sign = 1; string str; if(str1[0] == '-') { if(str2[0] == '-') { sign = -1; str = ADD_INT(str1.erase(0, 1), str2.erase(0, 1)); }else { str = MINUS_INT(str2, str1.erase(0, 1)); } }else { if(str2[0] == '-') str = MINUS_INT(str1, str2.erase(0, 1)); else { string::size_type l1, l2; int i; l1 = str1.size(); l2 = str2.size(); if(l1 < l2) { for(i = 1; i <= (int)(l2 - l1); i++) str1 = "0" + str1; }else { for(i = 1; i <= (int)(l1 - l2); i++) str2 = "0" + str2; } int int1 = 0, int2 = 0; for(i = str1.size() - 1; i >= 0; i--) { int1 = (int(str1[i]) - 48 + int(str2[i]) - 48 + int2) %10; int2 = (int(str1[i]) - 48 + int(str2[i]) - 48 +int2) / 10; str = char(int1 + 48) + str; } if(int2 != 0) str = char(int2 + 48) + str; } } //运算后处理符号位 if((sign == -1) && (str[0] !='0')) str = "-" + str; return str; }

“the way+从句”结构的意义及用法

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不对。 Theway(that ,in which)you’re doingit is comple tely crazy.你这么个干法,简直发疯。 Weadmired him for theway inwhich he facesdifficulties. Wallace and Darwingreed on the way inwhi ch different forms of life had begun.华莱士和达尔文对不同类型的生物是如何起源的持相同的观点。 This is the way(that) hedid it. I likedthe way(that) sheorganized the meeting. 3.theway(that)有时可以与how(作“如何”解)通用。例如: That’s the way(that) shespoke. = That’s how shespoke.

英语写作用词的准确表达

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