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In this work we examine the driving force for edge dislocations to climb in$\alpha$-Fe from atomistic and mesoscale viewpoints. We study the bias for theclimb process depending on the dislocation orientation and the applied stressas coming from both the gradient of the chemical potential and the transportcoefficients. Both terms are modified by the applied stress and thereforecontribute to climb. Surprisingly, even though the vacancy migration barrierdistribution is modified by the external stress as obtained by nudged-elasticband calculations, the mobilities resulting from a kinetic Monte Carlo modelapplied on the obtained energy landscape are indistinguishable, independentlyof the stress. Moreover, an object kinetic Monte Carlo (OKMC) model includingthe effect of the dislocation strain field to first order shows indeed a slightanisotropic component in the diffusion in more complex dislocationconfigurations. However, the OKMC results highlight the fact that thethermodynamic component is the dominant driving force. We conclude that in$\alpha$-Fe under thermal conditions, the main source of bias is given by thedifference in vacancy chemical potentials, which is small enough to hinder theprocess for dynamic atomistic simulations.

Relative relevance of mobility and driving force on edge dislocation climb by the vacancy mechanism