Figure 3 Top cross-sectional views of phase transformed region at different depths when nanoindenting on (101) germanium surface. At the depth of (a) approximately NVP-HSP990 solubility dmso 9 nm, (b) approximately 7 nm, (c) approximately 6 nm, and (d) approximately 5 nm from the top of the substrate. Figure 4 Side cross-sectional views of phase transformed region induced by nanoindenting on the (010) germanium surface. The surface is parallel to the (010) plane of (a) B1, (b) B2, and (c) B3 in Figure 3.

Figure 5 Top cross-sectional views of phase transformed region at different depths when nanoindenting on (111) germanium surface. At the depth of (a) approximately 9 nm, (b) approximately 7 nm, (c) approximately 6 nm, and (d) approximately 5 nm from the top of the substrate. Figure 6 Side cross-sectional views of phase transformed region induced by nanoindenting on the (111) germanium surface. The surface is parallel to the plane of (a) C1, (b) C2, and (c) C3 in Figure 5. Figure 7 Images of the structures formed during nanoindentation of monocrystalline germanium. (a) bct5-Ge structure, an enlarged view of D1 in Figure 2a. (b) β-tin-Ge structure, an enlarged view of D2 in Figure 2b. It is generally accepted that monocrystalline germanium transforms from a diamond cubic structure into a β-tin structure (Ge-II) during nanoindentation. Our study indicates that the Thiazovivin clinical trial process and

distribution of a structurally transformed phase are quite different when nanoindenting on various crystallographic orientation planes. In the case of nanoindentation on the (010) plane, the phase transformation from diamond cubic

structure into bct5-Ge (in cyan) occurs in the large areas surrounding the central place. The Ge-II structure (in yellow) initially appears centrally at the subsurface region beneath the indenter instead of at the region right under the tool. The atoms with coordination number 4(in black circles) shown in Figures 1c and 2b are arranged as diamond cubic structure. The stress distribution beneath a spherical indenter was obtained by a previous 6-phosphogluconolactonase simulation, which shows that the maximum hydrostatic stress occurs at the surface while the maximum shear stress occurs beneath the surface during initial elastic deformation in nanoindentation with a spherical indenter [14]. In this study, the Ge-II phase initially forms at the region beneath the surface, which indicates that the hydrostatic stress is not the only determining factor for the phase transformation from diamond cubic-Ge to Ge-II, and deviatoric stress along certain directions would reduce the threshold stress triggering this phase transformation. This phenomenon is the same with that of nanoindentation on the (100) silicon surface [7]. The atomic structural details of Ge-II are shown in Figure 7b, which is an enlarged view of the region D2 in Figure 2b. The boundaries of different phases are mainly along the directions, all of which belong to the same < 110 > slip 4EGI-1 direction of germanium.