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Although many studies have focused on slip systems and texture development in MgSiO₃ pPv and pPv analogs, the dominant slip systems are still debated. In general, the slip plane tends to be better constrained than slip direction. Nonetheless, three sets of dominant slip systems have been proposed for pPv. These are slip on (010) planes, slip on (100), and/ or {110}〈10〉, and finally slip on the (001) plane.

Early studies proposed that slip should occur on the (010) plane based on the fact that this coincides with the layering of the SiO₆ octahedra in the pPv structure (Iitaka et al., 2004; Murakami et al., 2004; Oganov & Ono, 2004). Several theoretical calculations have also supported slip on (010) in pPv or pPv analog materials (Carrez et al., 2007b, 2007a; Goryaeva et al., 2015a, 2015b, 2016, 2017; Metsue et al., 2009). Experimental evidence for slip on the (010) plane in pPv is limited to the CaIrO₃ analog. Due to the fact that it is stable in the pPv structure at ambient or near‐ambient conditions (Rodi & Babel, 1965), CaIrO₃ has been the most studied for deformation mechanisms of the pPv structured compounds. In compression studies, CaIrO₃ develops a maximum at (010) in the IPF (Figure 2.5a; Hunt et al., 2016; Miyagi, Nishiyama, et al., 2008; Niwa et al., 2007). A wide range of experiments using the DAC, D‐DIA, and other large volume apparatus at pressure and temperature condition up to 6 GPa and 1300 K over a range of strain rates all find dominant slip on (010)[100] and (010)<u0w> (Table 2.1; Hunt et al., 2016; Miyagi, Nishiyama, et al., 2008; Miyajima et al., 2006; Miyajima & Walte, 2009; Niwa et al., 2007; Walte et al., 2007, 2009; Yamazaki et al., 2006).

Figure 2.5 Summary of the various textures types observed in post‐perovskite structured compounds over a range of pressure and temperature conditions. Textures are represented as equal area, upper hemisphere projection, inverse pole figures of the compression direction. Scale bar is in multiples of random distribution.

Evidence for (100) or and/ or {110}〈10〉 comes from theoretical calculations and two early DAC studies. First‐principles metadynamics and energetics of stacking faults predicted slip on {110}〈10〉 during the phase transformation from Brg to pPv (Oganov et al., 2005). Shortly thereafter, room temperature radial diffraction DAC experiments on MgGeO₃ pPv and MgSiO₃ pPv found textures characterized by (100) planes at high angles to compression (Figure 2.5b, c). Polycrystal plasticity modeling showed that these texture could be explained by slip on {110}〈10〉 and (100) planes (Merkel et al., 2006, 2007). It is important to note that both Merkel et al. (2006) and Merkel et al. (2007) converted to the pPv phase directly from the enstatite phase, and no change in texture was observed upon further pressure increase. Subsequent studies on MgGeO₃ pPv in the DAC using axial diffraction geometry (Okada et al., 2010) and radial diffraction geometry (Miyagi et al., 2011) found that alignment of (100) planes at high angles to compression resulted from the phase transformation from an enstatite starting material (Figure 2.5d). Further compression showed that the initial (100) transformation texture shifted to (001) (Figure 2.5e) upon deformation consistent with dominant slip on (001)[100] (Table 1; Miyagi et al., 2011; Okada et al., 2010).

Slip on (001) planes in the pPv structure is supported by several DAC experiments both at ambient conditions (Miyagi et al., 2010, 2011; Okada et al., 2010) and high temperature (Hirose et al., 2010; Wu et al., 2017). Miyagi et al. (2010) found in pPv synthesized from MgSiO₃ glass that an initial (001) texture was observed after conversion at 148 GPa. Upon compression to 185 GPa this texture doubled in strength, consistent with slip on the (001) plane (Table 2.1; Figure 2.5f). High‐temperature deformation experiments on MnGeO₃ pPv documented the development of a (001) texture during compression from 63 GPa to 105 GPa at 2000 K (Figure 2.5g; Hirose et al., 2010). Deformation textures consistent with (001) slip have also been documented in MgGeO₃ pPv (Figure 2.5e; Miyagi et al., 2011; Okada et al., 2010). More recently, Wu et al. (2017) observed in MgSiO₃ pPv a similar transformation texture to that of Merkel et al. (2007) (Figure 2.5h) followed by the development of a (001) texture during compression to 150 GPa at 2500 K (Figure 2.5i).

Experimental deformation of MnGeO₃ pPv, MgGeO₃ pPv, and MgSiO₃ pPv are all consistent with slip on (001) (Table 2.1; Figure 2.5e, f, g, i). There is no clear experimental evidence to support deformation on (100) or {110}〈10〉. Textures previously attributed to slip on (100) and {110}〈10〉 have been shown to be due to the transformation from enstatite to pPv (Figure 2.5d, h). The evidence that slip on (010)[100] is the dominant system in CaIrO₃ is clearly robust based on the large number of independent and consistent experimental results (Hunt et al., 2016; Miyajima et al., 2006; Miyajima & Walte, 2009; Niwa et al., 2007; Walte et al., 2007, 2009; Yamazaki et al., 2006). CaIrO₃ pPv has very different structural parameters than MgSiO₃ pPv, in terms of bond lengths, bond angles, and octahedral distortions (Kubo et al., 2008). Raman spectroscopy measurements have also indicated that bonding in CaIrO₃ pPv is different from other pPv structured compounds (Hustoft et al., 2008). First‐principles computations find CaIrO₃ pPv to have elastic properties and an electronic structure that are inconsistent with MgSiO₃ pPv (Tsuchiya & Tsuchiya, 2007). Finally, first‐principles calculations based on the Peierls‐Nabarro model indicate that MgSiO₃, MgGeO₃, and CaIrO₃ exhibit considerable variations in dislocation mobilities (Metsue et al., 2009). Thus, it is perhaps unsurprising that CaIrO₃ pPv appears to be a poor analog for the deformation behavior of MgSiO₃ pPv. This is unfortunate, as CaIrO₃ pPv is the only pPv to be systematically studied at high temperature and varied strain rates.