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Under isothermal conditions, compression experiments were conducted at low, constant velocities of 0 0.4 μm s−1 up to macroscopic stresses of about 13 kPa, followed by subsequent stress relaxation measurements.
Typically, cavitation was initiated in volume at the stress of 29 30 MPa, but in the skin of injected samples voids were observed even at the macroscopic stresses of 2 MPa only.
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The 311 reflection does, however, respond almost linearly to loading, and therefore it constitutes a suitable reflection for characterization of macroscopic stresses and strains by diffraction for the given conditions.
The experiment results are linked to possible failure mechanisms in order to obtain the critical macroscopic stresses which are expressed in terms of cumulative distribution functions.
The goal is to determine the macroscopic stress of spalling in function of loading time and damage level via a meso-macro approach.
The subject of this paper is identification of the physical mechanisms of spalling at low impact velocities for Ti 6Al 4V alloy and determination of the macroscopic stress of spalling via meso-macro approach.
A physical modeling based on a thermally activated nucleation process has been developed for predicting the macroscopic stress for generation of cavities as well as the one for initiating crystal shearing.
In the simplest one-dimensional (1D) heterogeneous structural hierarchy, a series of non-local and non-convex double-well continuum elements are employed to model the micro-instability and the macroscopic stress hysteresis of the material under uniaxial quasi-static stretching.
Micro-mechanics of failure is a theory that links constitutive materials (individual fibre, matrix and their interface) and a macroscopic stress response of composites (Ha et al. 2008).
From these microfields, the macroscopic stress and strain of the crystal at different stages of loading were calculated.
At the level of each grain, plastic deformation occurs by the standard mechanism of dislocation slip, and so (i) constitutive equations that relate dislocation motion to crystal deformation must be defined, and (ii) an averaging scheme that relates the response of individual crystals to the macroscopic stress-strain response of the polycrystal must also be defined.
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