Dislocation Dynamics and Plasticity by Professor Taira Suzuki, Professor Shin Takeuchi, Professor

Dislocation Dynamics and Plasticity by Professor Taira Suzuki, Professor Shin Takeuchi, Professor

By Professor Taira Suzuki, Professor Shin Takeuchi, Professor Hideo Yoshinaga (auth.)

In the Nineteen Fifties the direct statement of dislocations turned attainable, stimulat­ ing the curiosity of many learn employees within the dynamics of dislocations. This resulted in significant contributions to the knowledge of the plasticity of varied crys­ talline fabrics. in this time the examine of metals and alloys of fcc and hcp constructions constructed remarkably. specifically, the invention of the so-called in­ ertial impression attributable to the electron and phonon frictional forces tremendously inspired the quantitative figuring out of the energy of those steel fabrics. Statis­ tical stories of dislocations relocating via random arrays of element stumbling blocks performed a huge function within the above advances. those subject matters are defined in Chaps. 2-4. Metals and alloys with bcc constitution have huge Peierls forces in comparison to people with fcc constitution. the explanations for the hold up in learning elements with bcc constitution have been typically problems hooked up with the purification recommendations and with microscopic stories of the dislocation center. within the Seventies, those problems have been mostly triumph over by way of advancements in experimental recommendations and computing device physics. experiences of dislocations in ionic and covalent bonding fabrics with huge Peierls forces supplied infonnation concerning the center constructions of dislocations and their digital interactions with charged debris. those are the most topics in Chaps. 5-7.

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Extra resources for Dislocation Dynamics and Plasticity

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7. Collinear arrangement of a dislocation with solute atoms. 25]. The final expression, however, is not given in analytical form. 37 steady-state motion appears by repetition of such processes. Lbj2T. 4) is then rewritten as l5 b12)t/3 L= ( ~ T l5. 5) ' which is called Friedel's relation. Lb L 1 cos "2 ¢>c . 8) where Fmb = W, Fm being the maximum interaction force and W the maximum interaction energy. Here, notice that Fleischer and Friedel assumed the relation cos Ij2¢>c ~ 1, that is, their theory holds for weak obstacles, which will be clarified in Sect.

10] found that ilTns depends linearly on ila/ a, the rate of variation of the lattice parameter per unit concentration of solute atoms, but not on the rate of variation of the electron density. 3 Strain-Rate Dependence It is important to know whether ilTns is caused by the athermal or thermal process of dislocations surmounting point obstacles. Alers et al. 16] first tried to clarify this problem. As already explained in Chap. 3, the flow stress of crystals is determined by the distribution and strength of obstacles.

191MNm- 2 for Is were applied. 13]. Pits of the largest, medium, and smallest sizes correspond to the positions of dislocations before loading. 001s 40 30 ~ lS00 20 10 (b) 200 400 600 d (,urn) 800 1000 Fig. 9a,b. Histograms of the number of moved dislocations vs the distance of movement. 56Tc for 5 X 10-4 s, respectively. 78Tc for 10-3 s. 7] move as much (as illustrated by A or B). The etch-pit method is inherently one to observe the surface of a specimen crysta1. 9 may therefore be doubtful, because the inner parts of the dislocations may move much larger distances than those expected from the observations of etch pits.

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