Plastic Rheological Behaviors of Zr61Cu25Al12Ti2 and Zr52.5Cu17.9Ni14.6Al10Ti5 Amorphous Alloys in the Supercooled Liquid Region
LIU Shuaishuai, HOU Chaonan, WANG Engang, JIA Peng()
Key Laboratory of Electromagnetic Processing of Materials (Ministry of Education), School of Metallurgy, Northeastern University, Shenyang 110819, China
Cite this article:
LIU Shuaishuai, HOU Chaonan, WANG Engang, JIA Peng. Plastic Rheological Behaviors of Zr61Cu25Al12Ti2 and Zr52.5Cu17.9Ni14.6Al10Ti5 Amorphous Alloys in the Supercooled Liquid Region. Acta Metall Sin, 2022, 58(6): 807-815.
The plastic deformation of amorphous alloys at room temperature is limited to small shear band zones and minimal strain. However, amorphous alloys in the supercooled liquid region exhibit superplasticity and have high forming ability. Zr61Cu25Al12Ti2 (ZT1) and Zr52.5Cu17.9Ni14.6Al10Ti5 (Vit105) amorphous alloys have excellent forming ability and similar mechanical properties at room temperature or low temperature. They have broad application prospects as flexible components, but little work has been conducted on the superplasticity of ZT1. This work examined the rheological behavior of the supercooled liquid of two amorphous alloys to provide a theoretical basis for microplastic deformation. ZT1 and Vit105 amorphous alloys were prepared by copper mold suction casting. The high-temperature rheological behaviors of the two amorphous alloys were investigated using Gleeble3500. Variations in temperature and strain rate influence the steady-state stress obviously in the supercooled liquid region. Theological transformation behaviors of the different Zr-based amorphous alloys were analyzed based on the viscous flow model. The plastic deformation in the supercooled liquid region included brittle fracture caused by local shear in low-temperature range or at a high strain rate, non-Newtonian rheology at high strain rates in the middle-temperature range, and Newtonian rheology at low strain rates in the high-temperature range. In the plastic deformation process at a low strain rate, nanocrystals are formed inside the amorphous alloy due to the combined actions of thermal and stress driving forces. With a compressive rate less than 1 × 10-3 s-1, ZT1 and Vit105 exhibited Newtonian flow over the temperature ranges of 678-703 K and 703-738 K, respectively. According to the free volume model, the calculated activation volumes for ZT1 and Vit105 were 0.137-0.590 nm3 and 0.123-0.234 nm3, respectively. The much smaller activation volume in Newtonian flow was associated with the higher diffusibility and atomistic mobility of the free volume in the material. The Vit105 amorphous alloy showed higher stability and glass formability, which is more convenient for thermoplastic processing, due to the combination of a high glass transition temperature and fragility parameter.
Fig.1 XRD spectra (a) and DSC curves (b) of Zr61Cu25Al12Ti2 (ZT1) and Zr52.5Cu17.9Ni14.6Al10Ti5 (Vit105) amorphous alloys (Tg and Tx are the glass transition temperature and crystallization temperature, respectively)
Fig.2 True stress-strain curves of ZT1 (a) and Vit105 (b) amorphous alloys at different temperatures with constant strain rate of 1 × 10-3 s-1
Fig.3 XRD spectra of ZT1 amorphous alloy at 688 and 693 K, and Vit105 amorphous alloy at 723 K after thermoplastic compressive deformation with constant strain rate of 1 × 10-3 s-1
Fig.4 True stress-true strain curves of ZT1 (at 663 K) (a) and Vit105 (at 683 K) (b) amorphous alloys with different strain rates
Fig.5 Steady-state stresses of ZT1 (a) and Vit105 (b) amorphous alloys as a function of strain rate at different temperatures
Fig.6 Variation relationships of the flow stress with the applied strain rate in ZT1 (a) and Vit105 (b) amorphous alloys at different temperatures (The solid lines are deduced from Eq.(1))
Fig.7 Viscosity change curves of ZT1 (a) and Vit105 (b) amorphous alloys
Fig.8 Boundaries between Newtonian flow to non-Newtonian flow for ZT1 and Vit105 amorphous alloys (T—experimental temperature)
Fig.9 Deformation maps of ZT1 (a) and Vit105 (b) amorphous alloys in the supercooled liquid region
Fig.10 Dependence of viscosity in the temperature in the supercooled liquid region of amorphous alloys (The fitting curves are deduced from Eq.(3). ηVFT—pre-exponential factor, D*—fragility parameter, T0—VFT temperature)
Fig.11 Angell diagram of the Newtonian viscosity of ZT1 and Vit105 amorphous alloys, where the temperatures are normalized by (Dc is the experimentally observed glass forming ability of the alloy expressed in terms of the maximum reported diameter of a rod, dmax (in mm); is the temperature in the MGs at which the equilibrium viscosity was determined to have a value of 1012 Pa·s; the dash lines are deduced from Eq.(3))
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