Low-frequency internal friction of α+β titanium alloy SP-700

Guan, X.S.; Numakura, Hiroshi; Koiwa, M.; Hasegawa, Kouki; Ouchi, Chiaki

doi:10.1016/s0921-5093(99)00464-5

Cited by 8 publications

(7 citation statements)

References 10 publications

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“…This activation energy is in good agreement with the values reported previously for relaxation processes in Ti-6-4, as shown in Table 3. Critically, this value is also similar to the activation energy reported for the diffusion of hydrogen in the β phase of pure titanium [41,42] and Ti-13V-11Cr-3Al [43]. Therefore, the acoustic loss peak appears to be associated with a Snoek-like relaxation of hydrogen in the β phase of Ti-6-4, as suggested previously [9][10][11].…”

Section: Acoustic Lossessupporting

confidence: 88%

On the effect of hydrogen on the elastic moduli and acoustic loss behaviour of Ti-6Al-4V

Driver

Jones

Stone

et al. 2016

Philosophical Magazine

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The elastic moduli and acoustic loss behaviour of Ti-6Al-4V (wt.%) in the temperature range 5-298 K have been studied using Resonant Ultrasound Spectroscopy. A peak in the acoustic dissipation was observed at 160 K within the frequency range 250-1000 kHz. Analysis of the data acquired in this study, coupled with complementary data from the literature, showed that this was consistent with a Snoeklike relaxation process with an associated activation energy of 23 ± 3 kJ mol −1 . However, the loss peak was broader than would be expected for a Snoek-like relaxation, and the underlying process was shown to have a spread of relaxation times. It is suggested that this effect arises as a result of variations in the strain experienced by the β phase due to different local microstructural constraint by the bounding secondary α phase. ARTICLE HISTORY

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Section: Acoustic Lossessupporting

confidence: 88%

On the effect of hydrogen on the elastic moduli and acoustic loss behaviour of Ti-6Al-4V

Driver

Jones

Stone

et al. 2016

Philosophical Magazine

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“…10) when the DIM is also increased in the same order indicates that the increase of fracture toughness is mainly due to the DIM as has also been observed by Niinomi et al. 14) in some commercial titanium alloys. The relatively higher fracture toughness of the specimens having lattice parameter of b phase larger than 0.323 nm (stable b phase) when the observed b phase contains coarse secondary phase indicates that the high fracture toughness in this case is mainly due to the secondary phase.…”

Section: Effect Of Stability Of Bsupporting

confidence: 74%

Effect of .BETA. Phase Stability at Room Temperature on Mechanical Properties in .BETA.-Rich .ALPHA.+.BETA. Type Ti-4.5Al-3V-2Mo-2Fe Alloy.

et al. 2002

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The stability of the b phase at room temperature in various microstructures of a b-rich aϩb type Ti-4.5Al-3V-2Mo-2Fe alloy and its relationship with the fracture toughness, hardness and tensile properties were investigated. A variety of microstructures were established by varying solution treatment temperatures in aϩb field, cooling rate after solution treatment and the condition of subsequent second-step annealing treatment after air-cooling treatment. These microstructures have b phase with lattice parameters of b phase ranging between 0.3244 nm and 0.3221 nm. The stability of b phase, which is indicated by decreasing lattice parameter of b phase, is increased by either lowering cooling rate or formation of diffusional transformation products (secondary phases) in the b phase. The b phase with lattice parameter of b phase around 0.3242 nm is the minimal instability of unstable b phase at room temperature for attaining deformation-induced martensite in tensile specimens. There exists a proper degree of b phase stability for increasing the fracture toughness, J IC . The relatively higher fracture toughness is obtained at low or high stability of b phase. The high fracture toughness at low stability of b phase (unstable b) is mainly due to the deformation-induced martensite. While, the high fracture toughness at high stability of b phase (stable b) is mainly due to the secondary phase in the b phase that produces a prominent crack deflection toughening mechanism. However, the relatively lower fracture toughness is obtained at high stability of b phase when the b phase contains small amount or no secondary phase. This leads to conclude that, if only the b phase stability is taken into account for explaining fracture mechanism, the fracture toughness would decrease monotonously with increasing stability of b phase. The Vickers hardness is nearly independent of stability of b phase.KEY WORDS: mechanical properties; fracture toughness; hardness; tensile properties; stability of b phase; microstructure; b-rich aϩb titanium alloy; Ti-4.5Al-3V-2Mo-2Fe.

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“…3), a well resolved peak having roughly the same activation energy of that in the Ti6Al4V alloy is present. Measurements performed at low frequency [12] yield similar activation energy. The prominent P 1 peak can be therefore attributed to a Snoek type relaxation caused by interstitials hydrogen atoms in the ␤ phase.…”

Section: Peak P1 P2mentioning

confidence: 60%