Fig. 2: Slip traces and dislocation structures in VNbMoTaW and TiZrNbHfTa after compression to 2 ~ 3% strain.
From: Intrinsic factors responsible for brittle versus ductile nature of refractory high-entropy alloys
a, b ψ-χ plots for VNbMoTaW (a) at room temperature and TiZrNbHfTa (b) at room temperature and 77 K (ψ-χ are defined in Supplementary Fig. 2). c–e Typical deformed micropillars of VNbMoTaW after loading along \([1\,2\,52]\)(c), \([\bar{5}\,8\,20]\)(d), and \([\bar{3}\,4\,4]\)(e). f–h Typical deformed micropillars of TiZrNbHfTa after loading along \([1\,2\,36]\)(f), \([0\,1\,2]\)(g), \([\bar{3}\,7\,8]\)(h). i, j Bright-field TEM images of typical deformation microstructure in VNbMoTaW afterslip on \((\bar{2}\,1\,1)\) (i) and \((\bar{1}\,0\,1)\) (j) at room temperature. k, l Bright-field TEM images of typical deformation microstructure in TiZrNbHfTa afterslip on \((\bar{2}\,1\,1)\) at room temperature (k) and 77 K (l). The thin foil for (k) was cut parallel to the \((\bar{2}11)\) macroscopic slip plane of the micropillar specimen deformed along the twinning direction. For comparison, (l) was cut parallel to the same plane from a deformed bulk polycrystal.
