Effect of mechanical alloying modes on the microstructure, phase composition and mechanical properties of powder high-entropy Co–Cr–Fe–Ni–Ti alloys

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Дәйексөз келтіру

Толық мәтін

Ашық рұқсат Ашық рұқсат
Рұқсат жабық Рұқсат берілді
Рұқсат жабық Тек жазылушылар үшін

Аннотация

The influence of the duration of mechanical alloying (15, 30, 45, and 60 min), the Ti content (4, 8, and 12 at %), and the method of its adding (in the form of Ti metal powder or TiH2 powder) on the microstructure, phase composition, and mechanical properties of Co–Cr–Fe–Ni–Ti high-entropy alloys (HEAs) manufactured by powder technology has been studied. It has been established that the structure of powder mixtures attains a high degree of homogeneity within 30 min of mechanical alloying and contains 43 and 57% of BCC and FCC phases, respectively. In the process of subsequent hot pressing, the structure is further homogenized, and the FCC phase content increases, reaching 99% in the alloys manufactured with TiH2. The optimal combination of mechanical properties is attained in the CoCrFeNiTi : the hardness is 74 HRA, and the ultimate tensile and bending strength are 690 and 1255 MPa, respectively. In the group of alloys made with Ti metal powder, the strength, hardness, density, and wear resistance grow, and brittleness decreases. To further improve the mechanical properties of Co–Cr–Fe–Ni–Ti HEAs manufactured using powder technology, it is necessary to optimize the σ-phase content and decrease the oxynitride phase content, which can be achieved both by adjusting the composition and by improving the modes of mechanical alloying.

Толық мәтін

Рұқсат жабық

Авторлар туралы

М. Berezin

National Research Technological University MISiS

Хат алмасуға жауапты Автор.
Email: berezinmaximus@gmail.com
Ресей, Moscow

А. Zaitsev

National Research Technological University MISiS

Email: berezinmaximus@gmail.com
Ресей, Moscow

B. Romanenko

National Research Technological University MISiS

Email: berezinmaximus@gmail.com
Ресей, Moscow

Р. Loginov

National Research Technological University MISiS

Email: berezinmaximus@gmail.com
Ресей, Moscow

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2. Fig. 1. SEM images of the microstructure of CoCrFeNiTi4, CoCrFeNiTi8 and CoCrFeNiTi12 powders after 15, 30, 45, 60 min ML. Cracks in the particles are outlined with a red dashed line.

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3. Fig. 2. Distribution of elements in CoCrFeNiTi4, CoCrFeNiTi8 and CoCrFeNiTi12 powders after 15 min ML.

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4. Fig. 3. MRSA results: from the surface of a section of CoCrFeNiTi4 powder particles after 45 min ML (a); after 60 min ML (b); CoCrFeNiTi8 after 45 min ML (c); from points inside a CoCrFeNiTi12 powder particle after 60 min ML (d).

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5. Fig. 4. X-ray diffraction patterns of CoCrFeNiTi8 powders after 15, 30, 45 and 60 min of ML.

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6. Fig. 5. SEM images of microstructures of compacts CoCrFeNiTi4 (a), CoCrFeNiTi8 (b), CoCrFeNiTi12 (c), CoCrFeNiTi4(TiH2) (d), CoCrFeNiTi8(TiH2) (d), CoCrFeNiTi12(TiH2) (e). Single dark rounded inclusions, spherical inclusions with dark boundaries and clusters of small dark inclusions are outlined by red dashed, turquoise dotted and yellow solid lines, respectively.

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7. Fig. 6. Results of MRSA of compacts: CoCrFeNiTi4 — from the surface of the section (a); CoCrFeNiTi4 — from selected points (b, c); CoCrFeNiTi8 — from the surface of the section (d); CoCrFeNiTi8 — from selected points (d); CoCrFeNiTi12 — from the surface of the section (e); CoCrFeNiTi12 — from selected points (g, h).

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8. Fig. 7. Results of MRSA of compacts: CoCrFeNiTi4(TiH2) — from the surface of the section (a); CoCrFeNiTi4(TiH2) — from selected points (b-d); CoCrFeNiTi8(TiH2) — from the surface of the section (d); CoCrFeNiTi8(TiH2) — from selected points (e); CoCrFeNiTi12(TiH2) — from the surface of the section (g); CoCrFeNiTi12(TiH2) — from selected points (h).

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9. Fig. 8. X-ray diffraction patterns of Co–Cr–Fe–Ni–Ti compacts obtained by the GP method. The initial powder mixture contained Ti in the form of metallic powder (a) or in the form of TiH2 (b).

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10. Fig. 9. Microstructure of fractures of CoCrFeNiTi4 (a, d), CoCrFeNiTi8 (b, d), and CoCrFeNiTi12 (c, e) compacts after three-point bending tests. The initial powder mixture contained Ti in the form of metallic powder (a–c) or in the form of TiH2 (b–e).

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11. Fig. 10. Stress-strain graphs of Co–Cr–Fe–Ni–Ti alloys during three-point bending tests.

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12. Fig. 11. Friction force curves and wear track topography for samples containing 4, 8, 12% Ti. The initial powder mixture contained Ti in the form of metal powder (a) or in the form of TiH2 (b).

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