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This macroscopic strain is generated from both intrinsic lattice strain and extrinsic domain switching and/or phase transformations.
In this study, the macroscopic strain is taken account of elastic strain, macro-transformation strain and macro-temperature strain.
As classically, the non-linear dependence on the applied macroscopic strain is retrieved for the solution at the first order.
In this work we consider an optimal design problem for two-component fractured media for which a macroscopic strain is prescribed.
The resulting macroscopic strain is calculated by applying fracture mechanics to the microcracks considered as either tensile or, in the form of a crushing band, as compressive.
The orientation of the lamellar stacks is similar to the orientation of the crystallites, showing that the macroscopic strain is transferred to the microscopic dimensions efficiently.
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There was more stress relaxation than in the FTIR experiments because of the longer duration of the measurement, but approximately half of the applied macroscopic strain was recovered as crystallographic strain, i.e., as an increase in axial dimension c of the unit cell measured from the 004 reflection.
The large macroscopic plastic strain is attributed to the combination of dislocation-based slip deformation in the ductile phase and extensive shear banding in the intermetallic phase.
At the macroscopic scale, volume strain is defined as the trace of the finite strain tensor whose components are recorded in situ by means of a 2D video extensometer within a representative volume element situated at the center of the neck.
At the position of the micromodel the macroscopic strain state is dominated by the membrane strains; the rotations are very small (see Fig. 8) and are therefore ignored in the computation of the local displacement boundary conditions on the y = 4 d and x = d/2 planes.
The macroscopic strain tensor is obtained by strain integration on microplanes of all orientations at a point by using a homogenization process.
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