Research Paper: Nucleation and Propagation of Dislocations

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[. . .] Along with indicating a thermal activation process, we see that the current work performs the e-ect of such a pinning site which is considered to be very important and must also be considered apart from the athermal mechanically driven propagation as by numerous researchers (see Chen et al., 2003b; Budrovic et al., 2004). Talking about ledge structures and dislocation Burgers vector, the pinning sites are made by unfavorable combinations in MD simulations whereas other possible initiations in the experimental sections such as impurities can be imagined (Froseth et al., 2006).

To sum up the research it is recommended that the ledges and areas of mis-t are responsible in controlling the nature with respect to where and how dislocations nucleate and propagate along with the atomistic details of dislocation nucleation, propagation or absorption in nc grains as a role of temperature. Considering the process is different from a simple Frank, the dislocation activity modifies the structural specifications of the GB. We see that the outcomes show that dealing with rate-controlling mechanism of dislocation activity in nc materials, dislocation propagation can play an important role as dislocation nucleation should thoroughly be considered (Froseth et al., 2006).

Predictions of MD stimulations, that have proven to be highly effected by in depth atomic mechanisms in the GB and the inherent nano-scale grain size of nc metals, regarding propagation, nucleation and absorption of full dislocations in nc metals that left no doubts in the examples which has been presented in the previous sections. In GB the nucleation and absorption of dislocations within tiny and spatial dimensions in the control of non-crystalline sets strict restrictions on the proliferation of the dislocations through grains.

The fact that has been fully ignored is related to determining the critical size of grain by the usage of splitting distance for the beginning of full dislocation activity. This activity is basically the nucleation of the dislocation taking place heterogeneously as a single spatial and there is being a temporary separation of events of dislocations from the GB. This is differentiated in a sense that it is being generated from a Frank, which is created fully as a dislocation. The basis of determining the energetic aspect of this nucleation method and its achievement by keeping in view its general planar fault curves represents a model for cost of atomic slip named as Peierls-type that is required to nucleate the dislocation heterogeneously, and is not dependent on the formation of a full dislocation. Current work exhibits that it is definitely possible to envisage the type of dislocation, either extended or full dislocations whose observation will take place in MD simulation from the universal planar fault curve (Chen et al., 2003a; 2003b; Froseth et al., 2004).

The curved element of the dislocation combined with the pinning and image forces along with the structural relaxation of the GB happen to occur because of the full dislocation transition by nano sized grain. This creates the material state of the system differentiating from the prediction, while ignoring the process of nucleating the dislocations from the GB and assuming that there is an existence of fully formed dislocation (Froseth et al., 2004).

In order to grasp the whole method of full disruption pursuit as studied in MD imitation of metals, there is still need to develop the theories that are related to disruption nucleation procedure, curved character of disruption, GB arrangement of nucleation site and communication of disruption with GB. In case, if such a model can be searched, then there is still a controversy that exists about that the limitations of intrinsic in MD simulation (Yamakov et al., 2001; Budrovic et al., 2004; Froseth et al., 2004).


Budrovic ' Z, Van Swygenhoven H, Derlet PM, Van Petegem S, Schmitt B. Science 2004; 304:273.

Chen M, Ma E, Hemker KJ, Sheng H, Wang Y, Cheng X. Science 2003b; 300:1275.

Chen S, Spencer JA, Milligan WW. Acta Mater 2003a; 51:4505.

Derlet PM, Hasnaoui A, Van Swygenhoven H. Scr Mater 2003b; 49:629.

Derlet PM, Van Swygenhoven H, Hasnaoui A. Philos Mag 2003a; 83:3569.

Froseth A, Van Swygenhoven H, Derlet PM. Acta Mater 2004; 52:2259.

Froseth, A.G., Derlet, P.M. And Swygenhoven, H.V. (2004). Dislocations emitted from nanocrystalline grain boundaries: nucleation and splitting distance. Acta Materialia 52: 5863 -- 5870

Froseth, A.G., Derlet, P.M. And Swygenhoven, H.V. (2006). Nucleation and propagation of dislocations in nanocrystalline fcc metals. Acta Materialia 54: 1975 -- 1983

Van Swygenhoven H, Derlet PM, Budrovic Z, Hasnaoui AZ. Metallkd 2003; 94:1106.

Van Swygenhoven H, Derlet PM, Froseth AG. Nat Mater 2004; 3:399.

Van Swygenhoven H, Derlet PM, Hasnaoui… [END OF PREVIEW]

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Nucleation and Propagation of Dislocations.  (2011, April 18).  Retrieved May 25, 2019, from

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"Nucleation and Propagation of Dislocations."  18 April 2011.  Web.  25 May 2019. <>.

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"Nucleation and Propagation of Dislocations."  April 18, 2011.  Accessed May 25, 2019.