Stability of the dislocation substructure of α-titanium against deformation temperature variation in the range 4.2–293 K

Smirnov, A. R.; Moskalenko, V. А.

doi:10.1016/0956-7151(94)90201-1

Cited by 8 publications

(9 citation statements)

References 8 publications

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“…A further factor that should be considered in understanding the observations of Chichili et al [24] was the observations reported by Smirnov et al [35,36] They showed that the dislocation structure developed in titanium deformed at temperatures lower than 100 K was significantly different than the dislocation structure developed in the same material deformed to the same strain level at room temperature. During lowtemperature deformation, the material had long slip bands consisting of a-type screw dislocations and twins with few accumulated edge dislocations [35,36,37] However, the substructure at room temperature consisted mainly of random edge and screw dislocations in a configuration the authors called reorientation bands.…”

Section: Effect Of Deformation Twinning On Different Stages Of Strmentioning

confidence: 95%

“…During lowtemperature deformation, the material had long slip bands consisting of a-type screw dislocations and twins with few accumulated edge dislocations [35,36,37] However, the substructure at room temperature consisted mainly of random edge and screw dislocations in a configuration the authors called reorientation bands. During room-temperature reloading in the experiments of Chichili et al, both edge and screw dislocations would have equal mobility, resulting in more activity of screw dislocations.…”

Section: Effect Of Deformation Twinning On Different Stages Of Strmentioning

confidence: 99%

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Strain hardening due to deformation twinning in α-titanium: Mechanisms

Salem

Kalidindi

Doherty

et al. 2006

Metall Mater Trans A

232

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Section: Effect Of Deformation Twinning On Different Stages Of Strmentioning

confidence: 95%

Section: Effect Of Deformation Twinning On Different Stages Of Strmentioning

confidence: 99%

Strain hardening due to deformation twinning in α-titanium: Mechanisms

Salem

Kalidindi

Doherty

et al. 2006

Metall Mater Trans A

232

View full text Add to dashboard Cite

“…For the sample deep drawn at room temperature, the microstructure with reorientation bands (RBs) 25) is observed. In other words, the grains are re-oriented during the deformation and propagate into elongated grain with RBs under the applied stress as shown in the TEM micrograph of Fig.…”

Section: Microstructure In Low Operating Temperaturementioning

confidence: 99%

“…The increased temperature during deep drawing suffices to suppress the RBs bands formation substantially. Both the strain hardening rate 27) and the RBs formation rate 25) of CP-Ti decrease with increasing temperature. The drawability remains poor due to the low ductility at 100°C.…”

Section: Figures 7(a) and 7(b)mentioning

confidence: 99%

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Relation between Deformability and Microstructures in a Commercial Pure Ti Sheet Subjected to Dual-temperature Square-shaped Deep Drawing.

2001

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Recent studies indicated that the deep drawing process at dual-temperatures could extend the drawability in many materials. This paper reports the study of commercial pure Titanium (CP-Ti)(a-Ti) heated to the temperature range of 25-400°C and deep-drawn by water-cooled square-shaped punch. The CP-Ti exhibits almost triple drawability when the temperature is increased from room temperature to 400°C. The location of the fracture point of CP-Ti sheets is on the corner of the cup wall near the die throat. The poor drawability at low temperature is due to the strain-hardening caused by reorientation bands (RBs). The active slip system at elevated temperature promotes the drawability of CP-Ti. The X-ray diffraction studies show the tendency of slip system to be active on the prismatic plane at ϳ200°C and on the pyramidal plane at ϳ400°C. The process at 400°C shows the microstructure with the micro-shear bands (MSBs) intersection induced by the heated die and the cooled punch. The MSB-MSB intersection prevents the further thinning of the cup wall and results in the superior deep drawability by virtue of better ductility.

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Damage process in commercially pure α-titanium alloy without (Ti40) and with (Ti40-H) hydrides

Huez

Helbert

Feaugas

et al. 1998

Metall Mater Trans A

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The influence of hydrostatic stress and hydrogen content on damage process was investigated in ␣titanium alloy. In particular, void site, void nucleation criterion, void nucleation, and void growth kinetics were experimentally determined. Void nucleation and growth rates and fracture process have been discussed using a Gurson-Tvergaard model. The main result is that void growth rate is not affected by hydride inclusions contrary to the void nucleation kinetic. In Ti40, the nucleation process has less influence than the growth process, which involves fracture. On the contrary, with regard to Ti40-H, the growth process is negligible and the nucleation kinetics, which is predominant, is the main cause of fracture.

show abstract

Stability of the dislocation substructure of α-titanium against deformation temperature variation in the range 4.2–293 K

Cited by 8 publications

References 8 publications

Strain hardening due to deformation twinning in α-titanium: Mechanisms

Strain hardening due to deformation twinning in α-titanium: Mechanisms

Relation between Deformability and Microstructures in a Commercial Pure Ti Sheet Subjected to Dual-temperature Square-shaped Deep Drawing.

Damage process in commercially pure α-titanium alloy without (Ti40) and with (Ti40-H) hydrides

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