Systems Titanium-Molybdenum and Titanium-Columbium

Hansen, M.; Kamen, E.L.; Kessler, H.D.; McPherson, D.J.

doi:10.1007/bf03397396

Cited by 31 publications

(14 citation statements)

References 2 publications

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“…3, with the experimental points. [40][41][42][43][44][45][46][47] 4.2 Thermodynamic analysis of the Nb-Ni-Ti ternary system and calculation of the phase diagrams Concerning the phase equilibria of the Nb-Ni-Ti system, Pryakhina et al 5) revealed incomplete isothermal section diagrams at 900 and 1000 C in the composition range between 50 and 100 mol%Ni. According to this experimental study, there are four types of ternary compound: Nb 15 1) investigated Nb 40Àx Ni 60 Ti x alloys by using X-ray diffraction, DSC, differential thermal analysis (DTA), and Vickers microhardness tests, and the liquidus lines at a constant Ti section were reported on.…”

Section: The Nb-ti Binary Systemmentioning

confidence: 99%

Thermodynamic Analysis of the Phase Equilibria of the Nb–Ni–Ti System

et al. 2005

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A thermodynamic analysis of the Nb-Ni-Ti system has been performed following the CALPHAD technique. To enable the thermodynamic description of the binary systems, the results from a previous evaluation were adopted for the Nb-Ni, Nb-Ti, and Ni-Ti systems. However, a slight modification of the parameters was applied to the bcc and Nb 6 Ni 7 phases in the Nb-Ni system, when considering the ternary phase equilibria. The phase boundaries of the Nb-Ni-Ti ternary system at a constant 28 mol%Ni and 60 mol%Ni were determined experimentally by differential scanning calorimetry. A thermodynamic assessment of the ternary system was performed based on the experimental information as well as the reported phase boundaries of the isothermal sections of the Nb-Ni-Ti system at 700, 800, and 900 C. Our calculations reveal that this system includes 15 types of ternary invariant reactions. The ternary eutectic temperature was between 901.6 and 1063.7 C.

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Section: The Nb-ti Binary Systemmentioning

confidence: 99%

Thermodynamic Analysis of the Phase Equilibria of the Nb–Ni–Ti System

et al. 2005

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“…For example, the addition of transition metals belonging to 8-, 9-and 10-groups in the Periodic Table reduces M s much significantly in comparison with those belonging to 5-group. [16][17][18][19][20][21][22][23][24][25][26] It was also reported that the phase transformation in -Ti alloys is affected by the density of d-electrons. 27) Thus, the addition of 3d-transition metals should change the phase stability of bcc and martensite phases due to the change in the d-electron density.…”

Section: Introductionmentioning

confidence: 99%

Effect of Cu Addition on Shape Memory Behavior of Ti-18 mol%Nb Alloys

et al. 2007

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Shape memory characteristics of Ti-18 mol%Nb alloys containing 3, 4, 5 and 6 mol%Cu (termed Ti18Nb3Cu, Ti18Nb4Cu, Ti18Nb5Cu and Ti18Nb6Cu, respectively) were investigated and effects of Cu addition on shape memory behavior was clarified. The alloys fabricated by Ar arc-melting method were cold-rolled with 98% reduction thickness and solution-treated at 1273 K for 1.8 ks followed by quenching into water. It was found by -2 X-ray diffraction analysis (XRD) at room temperature (RT) that Ti18Nb3Cu is composed of 00 (c-centered tetragonal)martensite phase and (bcc) parent phase. The other alloys with higher Cu contents are single phase. These results indicate that 6 mol%Cu is completely dissolved in Ti-18 mol%Nb alloys. Besides, the lattice parameter of phase is decreased by Cu addition with a rate of 0:2 Â 10 À3 nm/mol%Cu, and then, the atomic radius of Cu in Ti-18 mol%Nb alloys is estimated to be 0.130 nm. By tensile test it was found that (1) shape recovery strain of Ti18Nb3Cu reaches 3% by heating after deformation, (2) Ti18Nb4Cu exhibits superelasticity at RT, and (3) either shape memory effect or superelasticity does not appear at RT for Ti18Nb5Cu and Ti18Nb6Cu. Besides, the stress for slip deformation is increased by Cu addition with a rate of 50 MPa/mol%Cu. By tensile tests at cryogenic temperatures, the martensitic transformation start temperature (M s ) of Ti18Nb5Cu is determined to be 75 K, and the Cu addition to Ti-18 mol%Nb alloys decreases M s with a rate of 100 K/ mol%Cu. Moreover, more than 5% in transformation strain is observed for Ti18Nb5Cu at 173 K. It was concluded that Cu is an effective additional element in order to improve shape memory and superelastic properties of Ti-Nb alloys.

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“…pct V starting at about 15 at. pct of Hansen et al, [63] Adenstedt et al, [42] Duwez and Tay-V should be hypothesized in order to account for the data lor, [56] Levinger, [57] Pearson, [58] and Molchanov, [59] which in References 43 and 51. However, the possibility of such are listed in Table II.…”

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confidence: 99%

“…Of data for Ti-X systems, with X ϭ Zr, [61] Ta, [62] Cr, [56] Fe, [57] course, a negative deviation from linearity is also required and Mo. [63,64,51] In addition, extrapolations of the a ␤ vs T if one accepts the lowest a ␤ estimate for Ti. But the dashed data reported by Spreadborough and Christian [65] and by line in the inset suggests that such an effect would occur at Schmitz-Pranghe and Dunner [66] were performed in the lower V contents and would involve a difference of a ␤ for present study, using alternative assumptions about the temTi of about 0.4 pct, i.e., a small discrepancy.…”

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confidence: 99%

Metastable phases in the Ti-V system: Part I. Neutron diffraction study and assessment of structural properties

Aurelio

Guillermet

Cuello

et al. 2002

Metall Mater Trans A

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This article presents the results of a neutron diffraction study of a series of quenched Ti-V alloys and an assessment of the composition dependence of the structural properties in the Ti-V system. Upon quenching to room temperature and atmospheric pressure, three metastable phases occur, viz., the hcp (␣ Ј) phase formed by a martensitic transformation, the omega (⍀) phase formed by a displacive transformation involving the collapse of the (111) planes of the bcc structure, and the untransformed bcc (␤ ) phase. The lattice parameters (LPs) of the ␣ Ј, ␤, and ⍀ phases are determined as functions of the V content in the composition range 3 Յ at. pct V Յ 70. This information is combined with a detailed analysis of the available experimental data on the ␣ Ј, ␤, and ⍀ phases in pure Ti and Ti-V alloys and the ␤ phase of V. New estimates for the LPs of ␤ and ⍀ Ti and expressions describing the composition dependence of the LPs are presented. Using the assessed values, various open questions are discussed, i.e., the composition range where the hexagonal to trigonal symmetry change is observed in the ⍀ phase, the applicability of an approximation involved in the plane collapse model for the ␤ → ⍀ transformation, and the extent to which the so-called Jamieson correlation for interatomic distances in the ⍀ phase holds for Ti.

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Systems Titanium-Molybdenum and Titanium-Columbium

Cited by 31 publications

References 2 publications

Thermodynamic Analysis of the Phase Equilibria of the Nb–Ni–Ti System

Thermodynamic Analysis of the Phase Equilibria of the Nb–Ni–Ti System

Effect of Cu Addition on Shape Memory Behavior of Ti-18 mol%Nb Alloys

Metastable phases in the Ti-V system: Part I. Neutron diffraction study and assessment of structural properties

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Systems Titanium-Molybdenum and Titanium-Columbium

Cited by 31 publications

References 2 publications

Thermodynamic Analysis of the Phase Equilibria of the Nb&ndash;Ni&ndash;Ti System

Thermodynamic Analysis of the Phase Equilibria of the Nb&ndash;Ni&ndash;Ti System

Effect of Cu Addition on Shape Memory Behavior of Ti-18 mol%Nb Alloys

Metastable phases in the Ti-V system: Part I. Neutron diffraction study and assessment of structural properties

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Thermodynamic Analysis of the Phase Equilibria of the Nb–Ni–Ti System

Thermodynamic Analysis of the Phase Equilibria of the Nb–Ni–Ti System