Cryogenic wear behaviors of a metastable Ti-based bulk metallic glass composite

doi:10.1016/j.jmst.2022.06.027

Abstract

Abstract:

Bulk metallic glass composites (BMGCs) are proven to be excellent candidates for cryogenic engineering applications due to their remarkable combination of strength, ductility and toughness. However, few efforts have been done to estimate their wear behaviors that are closely correlated to their practical service. Here, we report an improvement of ∼ 48% in wear resistance for a Ti-based BMGC at the cryogenic temperature of 113 K as compared to the case at 233 K. A pronounced martensitic transformation (β-Ti→α″-Ti) was found to coordinate deformation underneath the worn surface at 233 K but was significantly suppressed at 113 K. This temperature-dependent structural evolution is clarified by artificially inducing a pre-notch by FIB cutting on a β-Ti crystal, demonstrating a strain-dominated martensitic transformation in the BMGC. The improved wear resistance and suppressed martensitic transformation in BMGC at 113 K is associated with the increased strength and strong confinement of metallic glass on metastable crystalline phase at the cryogenic temperature. The current work clarifies the superior cryogenic wear resistance of metastable BMGCs, making them excellent candidates for safety-critical wear applications at cryogenic temperatures.

Key words: Bulk metallic glass composites, Martensitic transformation, Cryogenic temperature, Wear

Yue Ren, Tingyi Yan, Zhuobin Huang, Qing Zhou, Ke Hua, Xiaolin Li, Yin Du, Qian Jia, Long Zhang, Haifeng Zhang, Haifeng Wang. Cryogenic wear behaviors of a metastable Ti-based bulk metallic glass composite[J]. J. Mater. Sci. Technol., 2023, 134: 33-41.

Figures/Tables 9

Fig. 1. (a) SEM microstructure and (b) corresponding XRD pattern of the Ti47.2Zr33.9Cu5.9Be13 BMGC.

Fig. 2. (a) TEM microstructure and corresponding SAEDs of metallic glass (upper) and β-Ti (lower) in the Ti47.2Zr33.9Cu5.9Be13 BMGC; (b) the HRTEM image of the interface between β-Ti and metallic glass; (c) the dark-field TEM micrograph and SAED pattern of the ω-Ti precipitates inside the β-Ti phase from [110]β-Ti zone axis; (d) the EDS mappings of β-Ti and metallic glass matrix.

Fig. 3. (a) Friction coefficient versus sliding time; (b) the variation of wear rates under varying cryogenic temperatures; (c) the three-dimensional morphologies and cross-sectional areas of worn surfaces at 233 K and 113 K.

Fig. 4. (a, b) Typical wear morphologies of BMGC tested at 233 K and 153 K, respectively; (c) EDS analysis of the worn surface after testing at 233 K.

Fig. 5. EDS analysis of the counterpart after testing at 233 K.

Fig. 6. (a) Overall cross-sectional microstructure of the BMGC after testing at 233 K; (b, c) enlarged α″-Ti structures under different depth; (d1, d2) dark-field TEM of α″-Ti and corresponding SAED pattern from zone axis [110]β-Ti; (e) HRTEM micrograph showing the boundary between α″-Ti and β-Ti/ω-Ti from the [110]β-Ti zone axis and corresponding FFT images of marked areas.

Fig. 7. (a) Overall subsurface microstructure of BMGC after testing at 113 K; (b1, b2) dark-field TEM of α″-Ti and corresponding SAED patterns from zone axis [111]β-Ti; (c1, c2) TEM micrograph and SAED patterns of the intact β-Ti phase, and (d) HRTEM image of boundary between the metallic glass and the intact β-Ti.

Fig. 8. (a) Selected area to perform a pre-notch by using the FIB cutting technique; (b) TEM observation of the artificially introduced pre-notch on the edge of the β-Ti grain; (c1) dark-field TEM micrograph of the parallel lath-shaped α″-Ti phase; (c2) SAED pattern of the target β-Ti after FIB cutting; (d) HRTEM image and attached FFT images of the newly formed α″-Ti phase.

Fig. 9. Mechanism for the abnormally suppressed martensitic transformation of BMGC at cryogenic temperatures.

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