  The plastic deformation mechanisms of tungsten carbide at room and elevated
temperatures influence the wear and fracture properties of WC-Co hardmetal
composite materials. Although the active slip planes and residual defect
populations of room-temperature deformed WC have been previously characterised,
the relationship between the residual defect structures, including glissile and
sessile dislocations and stacking faults, and the active slip modes, which
produce slip traces, is not yet clear. Part 1 of this study showed that {10-10}
was the primary slip plane at all temperatures and orientations. In the present
work, Part 2, crystallographic lattice reorientations of deformed WC
micropillar mid-sections were mapped using focused ion beam (FIB)
cross-sectioning and electron backscatter diffraction (EBSD). Lattice
reorientation axis analysis has been used to discriminate <a> prismatic slip
from multiple <c+a> prismatic slip in WC, enabling defect-scale deformation
mechanisms to be distinguished, and their contribution to plastic deformation
to be assessed, independently of TEM residual defect analysis. In
prismatic-oriented pillars, deformation was primarily accommodated by
cooperative multiple slip of <c+a> defects at room temperature, and by <a>
dislocations at 600 {\deg}C. In near-basal oriented pillars, the total slip
direction was along <c>. The degree of lattice rotation and plastic buckling in
the deformed basal pillar could be explained by prismatic slip constrained by
the indenter face and pillar base.
