Grain boundaries may contain special defects that only exist in grain boundaries; the most prominent ones are grain boundary dislocations. Grain boundary dislocations are linear defects with all the characteristics of lattice dislocations, but with very specific Burgers vectors that can only occur in grain boundaries.  
To construct grain boundary dislocations, we can use the universal Volterra definition.We start with a "low S" boundary and make a cut in the habit plane of the boundary. The cut line, as before, will define the dislocation line vector l which by definition will be contained in the boundary.  
Now we displace one grain with respect to the other grain by the Burgers vector b so as to preserve the structure of the boundary everywhere except around the dislocation line. In other words: the structure of the boundary after the shift looks exactly as before the shift.  
What does that mean? What is the "structure of the boundary" and how do we preserve it?  
Well, we have a CSL on both sides of the boundary. We certainly will preserve the structure of the boundary if we shift by a translation vector of the CSL, i.e. by a rather large Burgers vector. We than would preserve the coincidence site lattice  which is fine, but far too limited. We already preserve the structure of the boundary if we simply preserve the coincidence!  
It is best to illustrate what this means with a simple animation: Two superimposed lattices form a CSL marked in blue. The red lattice moves to the left, and at first there are no more coincidences of lattice points  the CSL has disappeared and we have a different structure. However, after a short distance of shifting  far smaller than a lattice vector of the CSL, coincidence points appears and we have a CSL again  but with the coincidence points now in different positions.  


We found a displacement vector that preserved the structure of the boundary  sort of experimentally. There are others, too, and the possible displacements vectors that conserve the CSL obviously are not limited to vectors of the crystal lattice; they can be much smaller. This we can generalize:  
The set of all possible displacement vectors which preserve the CSL defines a new kind of lattice, the socalled DSClattice. The abbreviation "DSC" stands for "Displacement Shift Complete", not the best of possible names, but timehonored by now.  
A better way of thinking about it would be to interprete the abbreviation as "Displacements which are Symmetry Conserving". Displacing one grain of a grain boundary with a CSL by a vector of the corresponding DSC lattice thus preserves the structure of the boundary because it preserves the symmetries of the CSL. We now conclude:  
Translation vectors of the DSC lattice are possible Burgers vectors b_{GB} for grain boundary dislocations. As for lattice dislocations, only the smallest possible values will be encountered for energetic reasons.  
Grain boundary dislocations constructed in this way by (Volterra) definition, have most of the properties of real dislocations  just with the added restriction that they are confined to the boundary. Strain and stress field, line energy, interactions, forming of networks  everything follows the same equations and rules that we found for lattice dislocations.  
It remains to be seen how the DSClattice can be constructed. From the illustration it is clear that every vector that moves a lattice site of grain 1 to a lattice site of grain 2 is a DSClattice vector. This leads to a simple "working" definition:  
The DSClattice is the coarsest sublattice of the CSL that has all atoms of both lattices on its lattice points. Most lattice points of the DSClattice, however, will be empty  

This is the DSClattice for the animation above. Its easy enough to obtain, but:  
A formal and general definition of the DSC lattice (including near CSL orientations) is one of the most difficult undertakings in grain boundary theory. If you love tough nuts, turn to chapter 7.3 and proceed.  
Any translation of one of the two crystals along a vector of the orange DSClattice will keep the CSL, but will generally shift its origin. Only if a DSC vector is chosen that is also a vector of the CSL, will the origin of the CSL remain in place.  
Looking back at the S5 boundary from before, we now can enact the cut and the displacement procedure and generate a picture of the dislocations that must result. The result contains a little surprise and is shown in crosssection below:  


The cut was made from the right. The top crystal (red lattice points) was shifted by a unit vector of the DSC lattice, which is a 1/5<210> vector in both crystal lattices in this case. The second crystal (green lattice points) was left completely unchanged. The coincidence points are blue. We observe two somewhat surprising effects:  
The boundary plane (as indicate by the pink line) after the shift is not identical with the plane of the cut  
The CSL has an interruption in both grains  it doesn't fit anymore. Disturbing  but totally unimportant. The CSL, after all, is totally meaningless for real crystals  the (mathematical) coincidence points in the grains have no significance for the grains. The only significance of a coincidence orientation is that it provides an especially good fit of the two grains at a boundary, i.e. it allows for a particularly favorable boundary structure. And the structure of the grain boundary is unchanged by the introduction of the grain boundary dislocation, except around its core region. This is indicated by the characteristic diamond shapes (yellow) in the picture above that can be taken as the hallmark of this S5 structure.  
Think about it! Finding the yellow diamonds is the practical way of finding the position of the boundary. However you define the position  you will find the preserved structure as expressed in the yellow diamonds here.  
Introducing the grain boundary dislocation thus had the unexpected additional effect of introducing a step in the grain boundary. Some atoms had to be changed from green to red to obtain the structure, but that again is an artifact of the representation. Real atoms are all the same; they do not come in green and red and do not care to which crystal they belong.  
We see that the recipe works: Dislocations in the DSC lattice preserve the structure of the boundary; they leave the coincidence relation unchanged. However, they also may introduce steps in the plane of the boundary we cannot yet be sure that this always the case.  
Note that is not directly obvious how the step relates to the dislocation, i.e. how the vector describing the step can be deduced from the DSC lattice vector used as Burgers vector. (If you see an obvious relationship  please tell me. I'm not aware of a simple formula applicable in all cases).  
Note also: While many (if not all) grain boundary dislocations are linked with a step, the reverse is not true: There are many possible steps in a boundary that do not have any dislocation character. More to that in chapter 8.3  
The extension to three dimensions is obvious, but also a bit mindboggling. Still, some general rules can be given  
The larger the elementary cell of the CSL, the smaller the elementary cell of the DSClattice!  
If you suspected it by now: The DSC lattice indeed can be seen as the reciprocal lattice (in space) of the CSL.  
The volumes of CSL, crystal lattice and DSC lattice relate as S : 1 : S^{ –1} for cubic crystals.  
What are all these lattices good for? The main import is:  
A grain boundary between two grains that is close to, but not exactly at a lowenergy (= low S) orientation may decrease its energy if grain boundary dislocations with a Burgers vector of the DSC lattice belonging to the lowS orientation are introduced so that the dislocation free parts are now in the precise CSL orientation and all the misalignment is taken up by the grain boundary dislocations.  
We will see how this works in the next subchapter. 
© H. Föll (Defects  Script)