Mechanical spectroscopy and twin boundary properties in a Ni50.8Ti49.2 alloy

Coluzzi, B.; Biscarini, A.; Campanella, R.; Trotta, L.; Mazzolai, Giovanni; Tuissi, A.; Mazzolai, F.M.

doi:10.1016/s1359-6454(99)00031-2

Cited by 71 publications

(34 citation statements)

References 16 publications

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“…The relative modulus change AER/EO, occurring between R s and Rf in the following denoted as "relative modulus defect", amounts to -31% and is expected to be due to the presence within the R martensite of mobile twin interfaces (AER/EO = (E(R S ) -E<Rf)/ E 0 ) [12]. The energy dissipation coefficient Q"'(T) is high in the B19' martensite and exhibits a well developed broad peak (PTWM) at around 130 K. The main features of the E(T) and Q"'(T) curves in figure 1 appear to be common to prior deformed and then aged NiTi/NiTiCu alloys and have already been reported [9,10] or will appear soon [11,12], thus, here only the E(T) and Q"'(T) behaviours above R s will be discussed.…”

Section: Resultssupporting

confidence: 61%

Nucleation of R-phase as studied by dynamic Young's modulus in the Ni₄₉Ti₅₁, aged alloy

et al. 2001

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Abstract. The Young's modulus E and the internal friction Q"' have been measured during thermal cycles carried out at temperatures higher than the start temperature R s (R s = 335 K) of the B2-> R martensitic transition in the Ni 49 Ti5i alloy, prior cold-worked (s = 32 %) and then aged at 673 K for 30 minutes. The cooling/heating E(T) and Q"'(T) branches of cycles extending down to the temperatures 350, 340 and 336 K exhibit progressively increasing thermal hysteresis, while those referring to a cycle only extending down to 369 K does not. This thermal hysteresis is attributed to the formation of stable nuclei of R martensite at dislocation or at some other type of lattice defects.

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Section: Resultssupporting

confidence: 61%

Nucleation of R-phase as studied by dynamic Young's modulus in the Ni₄₉Ti₅₁, aged alloy

et al. 2001

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“…[1][2][3][4][5][6][7][8][9][10][11][12][13][14][15][16][17][18] When heating and cooling TiNi-based SMAs, there is an internal friction (tan ) peak with a storage modulus (E 0 ) minimum corresponding to the martensitic transformation. 5) In addition, it has been reported that the formation of premartensite R-phase in TiNi-based SMAs can strongly soften the storage modulus and thus augment the internal friction during transformation.…”

Section: Introductionmentioning

confidence: 99%

“…Therefore, most of the internal friction studies of TiNi-based SMAs focus on the damping characteristics of IF Tr . [2][3][4][5][6][7][8][9][10][11][12][13][14][15][16][17][18] However, for high damping materials, it is more important to consider the damping characteristics of IF PT and IF I since most engineering applications for these materials are used at a constant temperature (especially at room temperature) instead of a constant temperature rate. Here, the term (IF PT +IF I ) is referred to as the inherent internal friction.…”

Section: Introductionmentioning

confidence: 99%

Inherent Internal Friction of Ti51Ni39Cu10 Shape Memory Alloy

Chang

2007

Mater. Trans.

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Ti 51 Ni 39 Cu 10 SMA is more suitable than Ti 50 Ni 50 SMA for use as a high damping alloy at room temperature because it has higher inherent internal friction and wider martensitic transformation temperature range. Experimental results show that tan values of both (IF PT +IF I ) B2!B19 and (IF PT +IF I ) B19!B19 0 of Ti 51 Ni 39 Cu 10 SMA are linearly proportional to 0 = 1=2 when the applied and 0 are within 10 Hz and 15 mm, respectively. Since defects and dislocations pin the martensite twin boundaries and obstruct their mobility, it is important to prevent the introduction of defects or dislocations into the solution-treated Ti 51 Ni 39 Cu 10 SMA to maintain its high inherent internal friction.

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“…7,9,14,15,17,19,23,30,[45][46][47][48][49][50][51][52][53]. Remaining questions to be answered are: a) the origin of the non-thermally activated peaks P 150K and P 200K and b) the role of H in the local strain glass transition.…”

Section: H-contaminated Materialsmentioning

confidence: 99%

Recent progresses in the understanding of the elastic and anelastic properties of H-free, H-doped and H-contaminated NiTi based alloys

Mazzolai¹

2011

AIP Advances

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This review is focused on the influence of interstitial hydrogen and alloy compositional changes on the internal friction (IF) spectrum and elastic Young's modulus (E) of NiTi based shape memory alloys. In the martensitically transforming binary alloys Ni50+xTi50-x (x≤1.3) vacuum annealed and furnace cooled (H-free), besides the well known IF peak associated with the martensitic transition two additional non-thermally activated peaks (P150K and P200K′) are present due to some sort of second-order phase transitions. In martensitically transforming Ni50+xTi50-x and Ti50Ni50-yCuy alloys doped with hydrogen two thermally activated peaks, PTWH and PH, appear which originate from stress-assisted motions of H-twin boundary complexes and isolated H-elastic dipoles (Snoek effect), respectively. In a H-free martensitically non-trasforming alloy (x=2), besides the non-thermally activated peak P150K, a frequency dependent dip is observed in the E(T) curves at a temperature Tg. This dip is similar to that reported in the literature for two other non-transforming alloys (x=1.5 and x=2.5), which, however, were also found to exhibit a thermally activated IF peak just below Tg. Most likely, these two alloys were contaminated with hydrogen during the preliminary solubilization in argon atmosphere and subsequent water quenching treatments given to them. The Young's modulus dip and the lower temperature IF peak have been both attributed to a novel type of phase transition reported in the literature as “strain glass transition”. The introduction of hydrogen into the non-transforming alloy with x=2 enhances the Young's modulus dip and gives rise to the H-Snoek peak PH just below Tg, which clearly appears to be the counterpart of the peak observed in the alloys (x=1.5 and x=2.5) solubilized in argon atmosphere and water quenched. The conclusion was reached in the present work that this last peak is not related to the strain glass transition but is rather an H-Snoek relaxation

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Mechanical spectroscopy and twin boundary properties in a Ni50.8Ti49.2 alloy

Cited by 71 publications

References 16 publications

Nucleation of R-phase as studied by dynamic Young's modulus in the Ni₄₉Ti₅₁, aged alloy

Nucleation of R-phase as studied by dynamic Young's modulus in the Ni₄₉Ti₅₁, aged alloy

Inherent Internal Friction of Ti<SUB>51</SUB>Ni<SUB>39</SUB>Cu<SUB>10</SUB> Shape Memory Alloy

Recent progresses in the understanding of the elastic and anelastic properties of H-free, H-doped and H-contaminated NiTi based alloys

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Mechanical spectroscopy and twin boundary properties in a Ni50.8Ti49.2 alloy

Cited by 71 publications

References 16 publications

Nucleation of R-phase as studied by dynamic Young's modulus in the Ni49Ti51, aged alloy

Nucleation of R-phase as studied by dynamic Young's modulus in the Ni49Ti51, aged alloy

Inherent Internal Friction of Ti<SUB>51</SUB>Ni<SUB>39</SUB>Cu<SUB>10</SUB> Shape Memory Alloy

Recent progresses in the understanding of the elastic and anelastic properties of H-free, H-doped and H-contaminated NiTi based alloys

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Nucleation of R-phase as studied by dynamic Young's modulus in the Ni₄₉Ti₅₁, aged alloy

Nucleation of R-phase as studied by dynamic Young's modulus in the Ni₄₉Ti₅₁, aged alloy