try Fundamental Aspects of Dislocation Theory: Conference Proceedings ..., Volume 1.

interesting, q. Background from Hull & Bacon Dislocation book:

"The shortest lattice vectors, and therefore the most likely Burgers

vectors for dislocations in the face-centred cubic structure, are of the type [110] and [001]. Since the energy of a dislocation is proportional to the square of the magnitude of its Burgers vector b^2, the energy of [110] dislocations will be only half that of [001], i.e. 2a^2/4  compared with a^.2 Thus, [001] dislocations are much less favoured energetically and, in fact, are only rarely observed. "

Strain hardening is due to the accumulation of dislocation barriers that act as obstacles to free dislocation movement. In FCC metals, immobile or sessile dislocations are the most abundant barrier and largely contribute to hardening behaviour. These can be created by dislocation interactions between dislocations on different glide planes. For each slip system of ½{111}[110], there are 18 possible dislocation interactions with another slip system on one of the other three glide planes (if you include the dislocation polarity). Some of these interactions can cause dislocation annihilation, and some can cause dislocation locks which form stable dislocation segments on crystallographic directions (such as [100] in the Hirth Lock or Lomer Lock) that are not slip directions. Since these directions do not allow slip, the dislocations become effectively locked and act as barriers to any nearby mobile dislocations that share the same slip system.

Check out Hull $ Bacon’s “Introduction to Dislocations” or Hirth and Lothe’s “Theory of Dislocations” for more.

Thanks Prof. Marian for your insightful reply. I'm enjoying the reading of your paper, it is really interesting and informative to learn dislocations in solids.

Anupam 

Thank you for correcting me Jaime, I have to say I'd never come across Hirth dislocations. I'll put your paper on my to do list, thanks for sharing