A study of structure of metastable Cu–Zn alloys with shape memory effect

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Methods of transmission and scanning electron microscopy are used to study premartenstic states and their relation to martensitic transformations in the alloys Cu–38 wt% Zn and Cu–39.5 wt% Zn with shape memory effect. Analysis of the observed diffusion scattering of electrons is carried out, including in situ experiments at heating and cooling and the defect condition of the internal substructure of austenite and martensite. The crystallographic models of martensitic transitions β2 →β2′, β2 →β2′′, and β2 →γ2′ are proposed based on the crystallographic data obtained in the premartensitic state.

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作者简介

A. Svirid

Mikheev Institute of Metal Physics, Ural Branch, Russian Academy of Sciences

编辑信件的主要联系方式.
Email: svirid@imp.uran.ru
俄罗斯联邦, Ekaterinburg, 620108

N. Kuranova

Mikheev Institute of Metal Physics, Ural Branch, Russian Academy of Sciences

Email: svirid@imp.uran.ru
俄罗斯联邦, Ekaterinburg, 620108

V. Pushin

Mikheev Institute of Metal Physics, Ural Branch, Russian Academy of Sciences

Email: svirid@imp.uran.ru
俄罗斯联邦, Ekaterinburg, 620108

S. Afanas’ev

Mikheev Institute of Metal Physics, Ural Branch, Russian Academy of Sciences

Email: svirid@imp.uran.ru
俄罗斯联邦, Ekaterinburg, 620108

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2. Fig. 1. OM (a), SEM (b), TEM images (bright- (d) and dark-field in the superstructure reflection 001B2 (c)) of the microstructure and microelectron diffraction patterns (with the zone axis (z.) [110]B2 (d) and [331]B2 (e)) of Cu–39.5Zn (a, c, d) and Cu–38Zn (b, d, e) alloys after quenching from 800°C for 30 min. The structure was studied at CT.

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3. Fig. 2. Bright-field TEM images of tweed contrast (a, b) and the corresponding microelectron diffraction pattern ((c) — o.z. [100]B2) of the two-phase (β2+3R)-alloy Cu–38Zn at RT.

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4. Fig. 3. Bright-field TEM images of tweed contrast (a, b) and corresponding microelectron diffraction patterns ((c) — [111]B2 RC and (d) — [110]B2 RC) of single-phase β2-alloy Cu–39.5Zn at RT.

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5. Fig. 4. Bright-field TEM images of tweed contrast (a, b) and corresponding microelectron diffraction patterns ((c) — o.z. [711]B2 and (d) — o.z. [311]B2) of single-phase β2-alloy Cu–39.5Zn at –100°C.

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6. Fig. 5. Spectra of atomic displacement waves in the form of flat cross sections (001)*, (110)*, and (111)* of the reciprocal k-space (a) and in the vicinity of the reciprocal lattice nodes in the (001)* and (110)* planes (b, c). The ek projections for k waves of increased amplitude and, consequently, more intense diffuse scattering are shown by dots, arrows, or dashes.

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7. Fig. 6. Schemes of shuffling displacements providing transformations of the cubic lattice B2 according to the PSS-I (a) and PSS-II (b) types in Cu–Zn alloys.

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8. Fig. 7. Intensity profiles during scanning of diffuse scattering along non-radial strands with satellites of the 1/6 <110>*, 1/3 <110>*, 1/2 <110>* type in microelectron diffraction patterns with the [100]B2 Cu–38Zn (a) and the [111]B2 Cu–39.5Zn alloy (b). Solid thin black lines represent intensity profiles, solid bold lines represent profiles calculated using the Gaussian function, dashed lines represent calculated profiles for satellites of the 1/6 <110>*, 1/3 <110>*, 1/2 <110>* type.

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9. Fig. 8. Light- (a, c) and dark-field (b) images of the microstructure of twinned β2′ (3R) (a, b) and long-period β2″ (9R) (c, d) martensite in the 3R reflection of the twin (with the [010]3R R.C. close to [111]B2) and the corresponding electron diffraction patterns ((b) — in the inset, (d) — with the [010]2H R.C. close to [111]B2) of the Cu–38Zn alloy.

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10. Fig. 9. Light- (a, c) and dark-field (b) TEM images of the microstructure of orthorhombic β2″(9R) (a, b, d, d) and hexagonal γ2′(2H) martensite (c, e) and the corresponding electron diffraction patterns (with R.E. [010]9R (d, e), close to [111]B2, and R.E. [010]2H (e)) of the Cu–39.5Zn alloy. Observations at a temperature of –150°C.

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11. Fig. 10. Schemes of the restructuring of the crystal lattice of the B2→3R (ABC), B2→9R (a) and B2→2H (AB) martensite (b) types in Cu–Zn alloys.

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