Download Dislocations in Solids, Vol. 15 by J.P. Hirth, L. Kubin (Eds.) PDF

By J.P. Hirth, L. Kubin (Eds.)

Bacon and Osetsky current an atomistic version of dislocation-particle interactions in steel platforms, together with irradiated fabrics. This paintings is necessary in simulating real habit, removal prior reliance on assumed mechanisms for dislocation movement. New mechanisms for dislocation iteration below surprise loading are offered by means of Meyers et al. those types offer a foundation for figuring out the constitutive habit of stunned fabric. Saada and Dirras offer a brand new standpoint at the Hall-Petch relation, with specific emphasis on nanocrystals. Of specific value, deviations from the normal rigidity proportional to the square-root of grain measurement relation are defined. Robertson et al ponder a couple of results of hydrogen on plastic stream and supply a version that offers an evidence of the vast diversity of homes.


  • Flow tension of steel platforms with particle hardening, together with radiation effects
  • New version for dislocation kinetics below surprise loading
  • Explanation of results of nanoscale grain measurement on strength
  • Mechanism of hydrogen embrittlement in steel alloys~

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Extra info for Dislocations in Solids, Vol. 15

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For larger voids, tc is controlled by the leading partial and the dislocation breaks away as a whole. Creation of a pure screw segment is not possible and dt/de does not decrease by dipole formation. As a consequence of these effects, voids in Cu are weaker obstacles than those in Fe when small and stronger when large. The latter effect arises from the high Peierls stress of one of the partials [120]. The dissociation of the core into distinct partials prevents dislocation climb, but it is possible that in metals with high stacking fault energy, such as Al, constriction of the core could result in dislocation–void interaction more like that in Fe.

DG* is the Gibbs free energy change at constant T and �_ between those two states. The probability of DG* being provided by thermal fluctuations is exp(�DG*/kBT) if DG*ckBT. Hence, from eq. J. Bacon et al. Ch. 88 Fig. 15. 51 nm. The dashed line indicates qtc/qT in the region of strong temperature-dependence. (From Ref. ) macroscopic plastic strain rate is   �DH* �_ ¼ rD A exp , kB T (10) where A ¼ bDn. D is the glide distance between each obstacle overcome and n the effective attempt frequency.

14), is tested for voids and precipitates in Fig. 26. Values of tc obtained in the continuum modelling of Refs [115,133,134] were found to fit eq. 52 for voids. Lines for these two values of D are drawn on Fig. 26. It is seen that the void data for Fe fit eq. e. just over 1 nm. tc for voids in Cu fall below the prediction of eq. 2 Dislocation–Obstacle Interactions at the Atomic Level 47 Fig. 26. 4–83 nm; Lx: 20–60 nm; number of atoms: 2–8 � 106). Lines obtained in Refs [115,133,134] as best fit to tc values obtained in continuum modelling for voids and impenetrable Orowan particles are also shown.

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