Fig. 4: Availability of {111}B1 slip in TiCx and TaCx.
From: Insights into the anomalous hardness of the tantalum carbides from dislocation mobility
Computed Peierls stresses for a TiCx and b TaCx on the {111}B1 and {110}B1 slip planes, with red squares indicating {111}B1 and blue triangles indicating {110}B1. c Computed stacking-fault widths, w, for TiCx and TaCx at different carbon contents. Narrow and wide stacking-faults, bounded by partial dislocations, are indicated by the figure insets: blue for TiCx and red for TaCx. d Dissociation of an edge dislocation with perfect Burgers vector b into a pair of Shockley partial dislocations with Burgers vectors bp1 and bp2 in a B1 crystal, showing an intrinsic stacking-fault formed between the partials. e The octahedral coordination environment seen in the B1 crystal. f The trigonal prismatic coordination environment of the Bh crystal. g The energy difference between Bh and B1 structures in TiCx (blue markers) and TaCx (red markers).
