# Elastic Strain Fields and Dislocation Mobility by V. L. Indenbom

By V. L. Indenbom

This quantity goals to supply an intensive remedy of the phenomena of elastic anisostropy and a dialogue on dislocation mobilities. The ebook provides a large remedy of those themes, and contains descriptions of targeted theoretical versions to explain dislocations and cracks, and relocating dislocations. an outline is given of the actual behaviour because of dislocation mobility in fabrics, equivalent to go with the flow and climb, interactions with element defects and the behaviour of dislocations less than radiation reminiscent of creep and swelling

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Consider the problem in the theory of cracks of the dislocation distribution in an arbitrary field of stresses. Let a crack form between two lines x = xx and x = x 2 in the plane y = 0. L. Indenbom 38 whereas the crack sides experience mutual displacement u^x). , I, II and III mode of fracture. The dislocation distribution az/(x) and the stresses σΙ7·(χ) in the plane y = 0 due to this distribution are related by the equations (the obvious sub scripts are omitted) £X- jam 2π _^ x — x or σ(χ') α(χ) = nAb άχ'.

117) the stresses given in eq. (120) determine the field of elastic displacements at the crack tip, - σ U(X) = — JL{X A v — Χχ) + · · · , 0 < Χχ — X <^ L. 6. The configuration force giving rise to crack propagation Now, let us consider the configuration force acting on the crack tip. By definition, this force is equal to the elastic energy which is released during crack propagation per unit length. This force may be calculated without considering the elastic stresses in the bulk of the body, by direct calculation of the work done by the stresses existing at the crack tip in front of the crack.

As can be seen from fig. 10, the angle of misorientation of blocks ω is defined by the ratio of Burgers vector b to distance h between the dislocations in the boundary, ω = b/h. (139) The dislocation structure of a subgrain boundary can generally be judged from the following relation, h^_dxj5i dxk Ί ckOk Wlj 9x f e ' (140) which can be obtained from eq. , $ij = 0. Switching from the lattice curvature δω,/δχ^ to the local bending at the subgrain boundary ωίη] (ω is the misorientation, and n is a normal to the boundary) and from the bulk to the surface distribution of dislocations, we find that ccfj = CDiUj - dij(uknk.