Comparison of the deformation behaviour of commercially pure titanium and Ti–5Al–2.5Sn(wt.%) at 296 and 728 K

Li, H.; Mason, D. E.; Yang, Yunfan; Bieler, T. R.; Crimp, M. A.; Boehlert, C. J.

doi:10.1080/14786435.2013.791752

Cited by 69 publications

(34 citation statements)

References 27 publications

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“…This is similar to that observed in 296 K tension tests of Ti-3Al-2.5 V plates [29]. Unlike that for 296 K tension-deformed CP Ti and Ti-5Al-2.5Sn, where some grains with Schmid factors below 0.1 were activated [30], prismatic slip was only observed when the Schmid factor was greater than 0.2. Most of grains that exhibited basal, pyramidal <a>, pyramidal <c + a> and twinning were also within regions where the Schmid factor was high.…”

Section: K Tension Specimen Asupporting

confidence: 74%

“…It is noted that no twinning has been observed during the deformation of Ti-8Al-1Mo-1V [31]. In our previous studies on CP Ti tensile deformed at 296 K [30], about 10% of the observed deformation systems was T1 twins. An even larger fraction of twins has been shown in CP Ti with increasing deformation for strains well above 10% [37][38][39][40][41].…”

Section: Twinningmentioning

confidence: 96%

“…This section compares the tensile-creep deformation behaviour of the currently examined Ti-6Al-4V to that for CP Ti and Ti-5Al-2.5Sn [30] and Ti-8Al-1Mo-1V [31]. During the elevated temperature tensile-creep tests, the relative activity of dislocation slip and GBS varied from material to material.…”

Section: Creepmentioning

confidence: 99%

“…The relative activity of pyramidal <a> and pyramidal <c + a> also changed with alloying. The pyramidal <a> slip system comprised less than 8% of the total deformation systems in CP Ti [30], Ti-5Al-2.5Sn [30] and Ti-6Al-4V (specimens A, B and C) at both 296 and 728 K. Compared to these alloys and Ti-8Al-1Mo-1V [31], there was slightly more pyramidal <c + a> slip activity in CP Ti at both 296 and 728 K, suggesting that the CRSS of pyramidal <c + a> slip increases with alloying content. The relative CRSS ratios, shown in Table 6 (discussed in more detail below), justify this statement.…”

Section: Twinningmentioning

confidence: 99%

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Examination of the distribution of the tensile deformation systems in tension and tension-creep of Ti-6Al-4V (wt.%) at 296 K and 728 K

Boehlert

Bieler

et al. 2015

Philosophical Magazine

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The deformation behaviour of an α + β Ti-6Al-4V (wt.%) alloy was investigated during in situ deformation inside a scanning electron microscopy (SEM). Tensile experiments were performed at 296 and 728 K (~0.4Tm), while a tensile-creep experiment was performed at 728 K and 310 MPa (σ/σ ys = 0.74). The active deformation systems were identified using electron backscattered diffraction-based slip-trace analysis and SEM images of the specimen surface. The distribution of the active deformation systems varied as a function of temperature. Basal slip deformation played a major role in the tensile deformation behaviour, and the relative activity of basal slip increased with increasing temperature. For the 296 K tension deformation, basal slip was less active than prismatic slip, whereas this was reversed at 728 K. Twinning was observed in both the 296 and 728 K tension experiments; however, no more than 4% of the total deformation systems observed was twins. The tension-creep experiment revealed no slip traces, however grain boundary ledge formation was observed, suggesting that grain boundary sliding was an active deformation mechanism. The results of this work were compared with those from previous studies on commercially pure Ti, Ti-5Al-2.5Sn (wt.%) and Ti-8Al-1Mo-1V (wt.%), and the effects of alloying on the deformation behaviour are discussed. The relative amount of basal slip activity increased with increasing Al content. IntroductionCompared with other structural metallic metals based on iron (Fe), nickel (Ni), aluminium (Al), and magnesium (Mg), titanium (Ti) has advantages of higher specific strength and exceptional corrosion resistance with a low density (ρ) of~4.5 g/cm 3 . Although Mg exhibits a density of~1.8 g/cm 3 , the disadvantages of low corrosion resistance, low melting point (650°C, 923 K) and relatively low yield strength (YS) make it less suitable than Ti for many structural applications. Al (ρ~2.7 g/cm 3 ) also exhibits the drawbacks of a low melting temperature (660°C, 933 K) and a low YS. Fe and Ni can overcome these disadvantages but the densities are nearly twice that of Ti. Thus, Ti and Ti alloys are currently employed in a variety of applications, including armor and

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Section: K Tension Specimen Asupporting

confidence: 74%

Section: Twinningmentioning

confidence: 96%

Section: Creepmentioning

confidence: 99%

Section: Twinningmentioning

confidence: 99%

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Examination of the distribution of the tensile deformation systems in tension and tension-creep of Ti-6Al-4V (wt.%) at 296 K and 728 K

Boehlert

Bieler

et al. 2015

Philosophical Magazine

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“…Characterization of the dislocation activity in J-TiAl intermetallics has been mostly carried out by transmission electron microscopy (TEM it facilitates the assignment of each slip trace to a specific slip system >31, [33][34][35], and, thus, the analysis of slip activity. This technique, which has not been utilized to date to investigate J-TiAl alloys, would clearly be very helpful to understand the links between the microstructure and the activation of different deformation mechanisms in this intermetallic.…”

Section: Introductionmentioning

confidence: 99%

Analysis of crystallographic slip and grain boundary sliding in a Ti–45Al–2Nb–2Mn (at%)–0.8vol%TiB2 alloy by high temperature in situ mechanical testing

Muñoz‐Moreno

Ruiz-Navas

Boehlert

et al. 2014

Materials Science and Engineering: A

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Analysis of crystallographic slip and grain boundary sliding in a Ti-45Al-2 Nb-2Mn (at. %)-0.8v.%TiB 2 alloy by high temperature in situ mechanical testing R. Muñoz-Moreno, E.M. Ruiz-Navas, C.J. Boehlert, J. Llorca, J.M. Torralba, M.T. Pérez-Prado PII:S0921-5093 (14) 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 galley proof before it is published in its final citable 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. AbstractThis work aims to contribute to a further understanding of the fundamentals of crystallographic slip and grain boundary sliding in the J-TiAl Ti-45Al-2Nb-2Mn (at.%)-0.8v.%TiB 2 intermetallic alloy, by means of in situ high-temperature tensile testing combined with electron backscatter diffraction (EBSD). Several microstructures, containing different fractions and sizes of lamellar colonies and equiaxed J-grains, were fabricated by either centrifugal casting or powder metallurgy, followed by heat treatment at 1300 ºC and furnace cooling. In situ tensile and tensilecreep experiments were performed in a scanning electron microscope (SEM) at temperatures ranging from 580 ºC to 700 ºC. EBSD was carried out in selected regions before and after straining. Our results suggest that, during constant strain rate tests, true twin J/J interfaces are the weakest barriers to dislocations and, thus, that the relevant length scale might be influenced by the distance between non-true twin boundaries. Under creep conditions both grain/colony boundary sliding (G/CBS) and crystallographic slip are observed to contribute to deformation. The incidence of boundary sliding is particularly high in J grains of duplex microstructures. The slip activity during creep deformation in different microstructures was evaluated by trace analysis. Special emphasis was placed in distinguishing the compliance of different slip events with the Schmid law with respect to the applied stress.

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The Effect of Aluminium on Deformation and Twinning in Alpha Titanium: The ND Case

Fitzner

Thomas

Fonseca

et al. 2016

Proceedings of the 13th World Conference on Titanium

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The deformation behavior of binary Ti-Al model alloys (0 to 13at.%) has been observed during compression normal to the rolling direction with respect to the activity of {1 1 2 2} compression twins but also the more common {1 1 2 0} tension twin as well as the rarely seen {1 1 2 1} tension twins. In-situ neutron diffraction loading experiments and EBSD microstructure analysis were used to qualify the impact of Al on twinning. The results show that for the given loading direction and starting texture,{1 1 2 2} and {1 1 2 0} twinning are similarly common in commercially pure Ti, while only small additions of Al result in a dramatic decrease in {1 1 2 2} compression twinning. In contrast, dramatic reductions of {1 1 2 0} twin fractions are only observed above 10at.% Al and with an ageing treatment to promote Ti 3 Al formation. Al addition until 10at.% makes {1 1 2 1} twinning more likely, but Ti 3 Al formation seems to deactivate this twin system. The role of slip on twinning is discussed.

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Comparison of the deformation behaviour of commercially pure titanium and Ti–5Al–2.5Sn(wt.%) at 296 and 728 K

Cited by 69 publications

References 27 publications

Examination of the distribution of the tensile deformation systems in tension and tension-creep of Ti-6Al-4V (wt.%) at 296 K and 728 K

Examination of the distribution of the tensile deformation systems in tension and tension-creep of Ti-6Al-4V (wt.%) at 296 K and 728 K

Analysis of crystallographic slip and grain boundary sliding in a Ti–45Al–2Nb–2Mn (at%)–0.8vol%TiB2 alloy by high temperature in situ mechanical testing

The Effect of Aluminium on Deformation and Twinning in Alpha Titanium: The ND Case

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