Mechanical properties of nanocrystalline Ti–Al–X alloys

Calderón, H.A.; Garibay-Febles, V.; Umemoto, Minoru; Yamaguchi, M.

doi:10.1016/s0921-5093(01)01568-4

Cited by 61 publications

(71 citation statements)

References 21 publications

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“…Itsukaichi et al [4] showed that an Al 50 Ti 50 amorphous alloy can be consolidated by hot pressing with temperature of 800 °C and pressure of 100 MPa for 600 s and this amorphous phase crystallize to an AlTi intermetallic compound. Calderon et al [5] consolidated Al 50 Ti 50 amorphous alloy by spark plasma sintering to form two intermetallic compounds, AlTi and AlTi 3 . …”

Section: X-ray Diffractionmentioning

confidence: 99%

Phase stability, porosity distribution and microstructural evolution of amorphous Al50Ti50 powders consolidated by electrical resistance sintering

Urban

Cuevas

Montes

et al. 2015

AIP Conference Proceedings

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The effect of intensity and duration of the electrical resistance sintering process on the phase stability, porosity distribution and microstructural evolution of Al50Ti50 amorphous powders is studied. The phase transformations during the consolidation process were determined by X-ray diffraction. The porosity distribution was observed by optical and scanning electron microscopy. The amorphous phase is partially transformed to the crystalline phase during the sintering process, and formation of AlTi and AlTi3 intermetallic compounds occurs for temperatures higher than 300 °C. Finally, it is observed that the compacts core have lower porosity and a higher tendency to the amorphous-crystalline phase transformation than the periphery

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Section: X-ray Diffractionmentioning

confidence: 99%

Phase stability, porosity distribution and microstructural evolution of amorphous Al50Ti50 powders consolidated by electrical resistance sintering

Urban

Cuevas

Montes

et al. 2015

AIP Conference Proceedings

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“…The stress and lattice parameters (note that a 2 = a 1 ) calculated under epitaxial tension (the epitaxial tetragonal path -ETP) as a function of the biaxial strain ε = ε 1 + ε 2 are represented by grey (brown) lines with open symbols. The results for the secondary orthorhombic path (SOP), starting by applying tension/compression to the stress-free bcc state B (2) on the ETP are shown by grey (blue) lines and full symbols. The thick dashed black lines represent the transformation from the bcc states B (1,2) to the fcc states F (1,2) under a shear deformation (cf.…”

Section: Fcc Metals Under Uniaxial [100] Loadmentioning

confidence: 99%

“…The results for the secondary orthorhombic path (SOP), starting by applying tension/compression to the stress-free bcc state B (2) on the ETP are shown by grey (blue) lines and full symbols. The thick dashed black lines represent the transformation from the bcc states B (1,2) to the fcc states F (1,2) under a shear deformation (cf. the discussion at the end of this section).…”

Section: Fcc Metals Under Uniaxial [100] Loadmentioning

confidence: 99%

“…Capital letters and vertical dotted lines mark special states discussed in the text. In the bottom panel showing the variation of the lattice constants the rectangles of thin dotted lines connect the stress-free states B (1) , T (1) and B (2) ,T (2) formed under uniaxial compression and epitaxial tension, respectively. As for the fcc metals the appearance of these states is symmetry-dictated, their structures are exactly identical.…”

Section: Fcc Metals Under Uniaxial [100] Loadmentioning

confidence: 99%

“…Trialuminides of early transition-metal (TM) elements (Al 3 TM, TM=Sc, Ti, V) are of great technological interest because of their potential applications as light-weight high performance structural materials [1][2][3]. However, their practical applications are limited because of high brittleness and poor ductility at room temperature.…”

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Response of fcc metals andL1₂andD0₂₂type trialuminides to uniaxial loading along [100] and [001]:ab initioDFT calculations

Jahnátek¹,

Krajčı́²,

Hafner³

2011

Philosophical Magazine

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Although the response of both pure fcc metals could be expected to be very similar, our results show a fundamental difference: whereas for Cu a special invariant state with C 22 = C 23 , leading to a bifurcation from the tetragonal to an orthorhombic deformation path, is reached at a strain of 10%, for Al this state is reached only at a strain of 33% close to the critical strain defining the ideal tensile strength. The reaction of the L1 2 -type trialuminides is comparable to the response of Al, no bifurcation to an orthorhombic deformation path is predicted.The response of the D0 22 -type trialuminides is different from that of the L1 2 -type phases because of the difference in the stacking of the atomic planes along the [001]. For D0 22 -type trialuminides, the uniaxial compression along this direction or epitaxial tension in the (001) leads to the formation of a stress-free D0 3 structure, in complete analogy to the fcc⇆bcc transformations observed for the pure metals. Under uniaxial [100] loading the guiding symmetry along the deformation path is orthorhombic and leads to the formation of special structures under both tension and compression parts, which are related to the D0 3 structure in the same way as the parent D0 22 -lattice to the L1 2 structure.

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Powder Metallurgy

2011

Gamma Titanium Aluminide Alloys

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Mechanical properties of nanocrystalline Ti–Al–X alloys

Cited by 61 publications

References 21 publications

Phase stability, porosity distribution and microstructural evolution of amorphous Al50Ti50 powders consolidated by electrical resistance sintering

Phase stability, porosity distribution and microstructural evolution of amorphous Al50Ti50 powders consolidated by electrical resistance sintering

Response of fcc metals andL1₂andD0₂₂type trialuminides to uniaxial loading along [100] and [001]:ab initioDFT calculations

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Mechanical properties of nanocrystalline Ti–Al–X alloys

Cited by 61 publications

References 21 publications

Phase stability, porosity distribution and microstructural evolution of amorphous Al50Ti50 powders consolidated by electrical resistance sintering

Phase stability, porosity distribution and microstructural evolution of amorphous Al50Ti50 powders consolidated by electrical resistance sintering

Response of fcc metals andL12andD022type trialuminides to uniaxial loading along [100] and [001]:ab initioDFT calculations

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Response of fcc metals andL1₂andD0₂₂type trialuminides to uniaxial loading along [100] and [001]:ab initioDFT calculations