Effect of Vanadium Concentration on the Structure and Properties of Ti–V Alloys Subjected to High-Pressure Torsion

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Abstract

The effect of preliminary annealing at 1000°C and subsequent high-pressure torsion (HPT) on the phase composition and mechanical properties of titanium alloys with 2, 4, 6, and 8 wt % V is studied. The increase in the V concentration in the initial alloy leads to an increase in the volume fraction of the β-Ti phase and a decrease in the volume fraction of the ω-Ti phase after HPT. The nanohardness Н and Young’s modulus Е were measured by nanoindentation. After HPT, the values of Н and Е are higher than those observed after preliminary annealing by 44 and 20%, respectively. The nanohardness and Young’s modulus of the studied alloy subjected to HPT are independent on the fraction of second constituent and are Н = 6.2 ± 0.2 GPa and Е = 138 ± 3 GPa, respectively. However, the hardness of the alloys subjected to HPT, which was measured by microindentation, also is independent of the fraction of the second constituent. At the same time, the ultimate strength and Young’s modulus measured by three-point bending technique have significant differences and, as the V concentration increases, decrease from 3.1 to 2.4 GPa and from 204 to 165 GPa, respectively. The decrease correlates with changing the volume fractions of the ω-Ti and β-Ti phases. The correlation between the vanadium content, phase composition, and ultimate strength of alloys subjected to HPT is found experimentally.

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About the authors

G. S. Davdian

Osipyan Institute of Solid State Physics RAS (ISSP RAS); National Research Technological University MISiS

Author for correspondence.
Email: faberest@yandex.ru
Russian Federation, Chernogolovka, Moscow Region, 142432; Moscow, 119049

A. S. Gornakova

Osipyan Institute of Solid State Physics RAS (ISSP RAS)

Email: faberest@yandex.ru
Russian Federation, Chernogolovka, Moscow Region, 142432

B. B. Straumal

Osipyan Institute of Solid State Physics RAS (ISSP RAS); National Research Technological University MISiS

Email: faberest@yandex.ru
Russian Federation, Chernogolovka, Moscow Region, 142432; Moscow, 119049

V. I. Orlov

Osipyan Institute of Solid State Physics RAS (ISSP RAS)

Email: faberest@yandex.ru
Russian Federation, Chernogolovka, Moscow Region, 142432

N. S. Afonikova

Osipyan Institute of Solid State Physics RAS (ISSP RAS)

Email: faberest@yandex.ru
Russian Federation, Chernogolovka, Moscow Region, 142432

A. I. Tyurin

Research Institute of Nanotechnology and Nanomaterials, Derzhavin Tambov State University

Email: faberest@yandex.ru
Russian Federation, Tambov, 392000

A. V. Druzhinin

Osipyan Institute of Solid State Physics RAS (ISSP RAS)

Email: faberest@yandex.ru
Russian Federation, Chernogolovka, Moscow Region, 142432

A. Kilmametov

Laboratory of Technological and Materials Research

Email: faberest@yandex.ru
France, Villetanez, 93430

S. Sommadossi

Institute of Research in Engineering Sciences and Technology, National University of Comahue, National Council for Scientific and Technological Research

Email: faberest@yandex.ru
Argentina, Buenos Aires 1400 (Q8300IBX), Neuquén — Patagonia, 1400

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Supplementary files

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2. Fig. 1. Volume fractions of α-, β- and ω-phases in Ti–V alloys after annealing (a) and after CVD (b).Based on the phase diagram of the Ti–V system, as the concentration of vanadium in the alloy increases, the proportion of the residual β-Ti phase should increase linearly. In our study, we observed the phase distribution shown in Fig. 1a. After CVD, the ω-Ti phase is also formed, the proportion of which ranges from 76 to 49%.

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3. Fig. 2. Radiographs of Ti–2 alloys weight. % V (a), Ti–4 weight. % V (b), Ti–6 weight. % V (V), Ti–8 weight. % V (d), where the black lines correspond to the annealed samples, and the red lines correspond to the samples after CVD.

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4. Fig. 3. Microstructures of Ti–2 alloys weight. % V (a), Ti–4 weight. % V (b), Ti–6 weight. % V (V), Ti–8 weight. % V (g) annealed at 1000°C.

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5. Риc. 4. ПЭМ-изображения микроструктуры сплавов в светлопольном (сверху), темнопольном (в центре) виде и их электронограммы (снизу) Ti–2 вес. % V (а–в), Ti–4 вес. % V (г–е), Ti–6 вес. % V (ж–и), Ti–8 вес. % V (к–м), после КВД.

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6. Fig. 5. Loading curves of Ti–V alloys in the CVD process.

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7. Fig. 6. Curves of Ti–V P-h alloys after annealing and after CVD, where T°C corresponds to 1000°C.

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8. Рис. 7. Твердость сплавов при наноиндентировании в зависимости от расстояния точки измерения от центра образца, для отожженных (черные квадраты) и обработанных КВД (красные квадраты) образцов An–2 вес. % V ( / ), Ti - 4//. % V ( / / ), Ti - 6//. % V ( / ), Ti - 8//. % V ( .. ).

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9. Fig. 8. Modulus of elasticity of alloys during nanoindentation as a function of the distance of the measuring point from the center of the sample, for annealed (black circles) and CVD–treated (red circles) samples Ti-2 weight. % V (a), Ti–4 weight. % V (b), Ti–6 weight. % V (V), Ti–8 weight. % V (y).

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10. Fig. 9. Average values of nanohardness (a) and modulus of elasticity (b) for annealed (black symbols) and treated CVD (red symbols) Ti–V samples under study.

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11. Fig. 10. Average microhardness values for annealed (black squares) and treated CVD (red squares) Ti–V samples under study.

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12. Fig. 11. Results of three-point bending tests of the most average annealed (a) and CVD-treated (b) samples.

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13. Fig. 12.Photographs of fractures of samples after CVD treatment formed during three-point bending tests: Ti–2 wt.% V (a, b), Ti–4 wt.% V (c, d), Ti–6 wt.% V (e, f) and Ti-8 weight% V (same, c).

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14. Fig. 13. Average grain size in Ti–V alloys after CVD.

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15. Fig. 14. Average values of (a) the conditional yield strength σ0.2 of annealed samples, (b) the tensile strength of the σB samples after CVD, (c) the bending modulus after annealing and after CVD, and (d) the maximum deformation before fracture of the samples after CVD, depending on the proportion of the second component (V) in the alloy.

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