“…The main idea of this transition method is to interpret the AS results as a function of the effective stress on the dislocation segment pinned by the precipitate. This approach has already been used in analytical approaches [5] and in DD simulations of precipitate hardening [27,30]. At zero K, the precipitate cannot keep a dislocation segment pinned when it is submitted to an effective stress s eff larger than a critical value, called the obstacle resistance s obs .…”
Section: From Atomistic Simulations To Dislocation Dynamicsmentioning
confidence: 99%
“…At zero K, the precipitate cannot keep a dislocation segment pinned when it is submitted to an effective stress s eff larger than a critical value, called the obstacle resistance s obs . For example, if the shearing process creates an antiphase surface, s obs is equal to c/b [27], where c is the antiphase surface energy and b the norm of the Burgers vector. s obs is naturally connected to the classical strength F obs by F obs ¼ Dbs obs , where D is the diameter of the precipitate, considered to be of spherical form in all AS and DD simulations.…”
Section: From Atomistic Simulations To Dislocation Dynamicsmentioning
confidence: 99%
“…These flaws can be overcome using the DD simulation technique, where precipitates of finite size of arbitrary distribution can be mapped into the simulation box and dislocation-dislocation interactions are fully accounted for. The first DD investigations of PH were reported by Flush et al [25] and Mohles et al [26] and extended later to different interaction mechanisms [27,28]. Although a thorough progress has been made in these studies, the interaction potential was not built using ASs.…”
“…The main idea of this transition method is to interpret the AS results as a function of the effective stress on the dislocation segment pinned by the precipitate. This approach has already been used in analytical approaches [5] and in DD simulations of precipitate hardening [27,30]. At zero K, the precipitate cannot keep a dislocation segment pinned when it is submitted to an effective stress s eff larger than a critical value, called the obstacle resistance s obs .…”
Section: From Atomistic Simulations To Dislocation Dynamicsmentioning
confidence: 99%
“…At zero K, the precipitate cannot keep a dislocation segment pinned when it is submitted to an effective stress s eff larger than a critical value, called the obstacle resistance s obs . For example, if the shearing process creates an antiphase surface, s obs is equal to c/b [27], where c is the antiphase surface energy and b the norm of the Burgers vector. s obs is naturally connected to the classical strength F obs by F obs ¼ Dbs obs , where D is the diameter of the precipitate, considered to be of spherical form in all AS and DD simulations.…”
Section: From Atomistic Simulations To Dislocation Dynamicsmentioning
confidence: 99%
“…These flaws can be overcome using the DD simulation technique, where precipitates of finite size of arbitrary distribution can be mapped into the simulation box and dislocation-dislocation interactions are fully accounted for. The first DD investigations of PH were reported by Flush et al [25] and Mohles et al [26] and extended later to different interaction mechanisms [27,28]. Although a thorough progress has been made in these studies, the interaction potential was not built using ASs.…”
“…Recently, Mohles et al [3,4,5] have performed numerous twodimensional dislocation dynamics (DD) simulations in which one or few dislocations glide in a plane intersected by many coherent precipitates, but at a low volume fraction. In addition, Rao et al [6,7] have carried out DD simulations on g/g 0 superalloys with up to 40 vol.% of coherent precipitates.…”
“…In their simulation they introduced the criterion to determine the instability of the dislocation configuration in terms of the spacing of any two face-to-face bowed-out dislocation segments. Mohles et al [14][15][16] simulated dislocation glide using the local stress equilibrium 18 of particles. They considered a constant volume fraction and varied the particle radii to obtain underaged (essentially shearable), over-aged (non-shearable), and peak-aged particles.…”
Aging of precipitation hardened alloys results in particle coarsening, which in turn affects the strength. In this study, the effect of particle size distribution on the strength of precipitation-hardened alloys was considered. To better represent real alloys, the particle radii were distributed using the Wagner and Lifshitz and Slyozov (WLS) particle size distribution theory. The dislocation motion was simulated for a range of mean radii and the critical resolved shear stress (CRSS) was calculated in each case. Results were also obtained by simulating the dislocation motion through the same system but with the glide plane populated by equal strength particles, which represent mean radii for each of the aging times. The CRSS value with the WLS particle distribution tends to decrease for lower radii than it does for the mean radius approach. The general trend of the simulation results compares well with the analytical values obtained using the equation for particle shearing and the Orowan equation.
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