Grain Boundary - Advanced

  Geometric Description of a Grain Boundary
For starters, we ask ourselves how we can describe the basic geometry of a nice planar grain boundary.
One way of tackling this is to cut (in your brain) one crystal in a plane that is to become the grain boundary plane in the starting crystal 1. The cut-off part we rotate arbitrary amounts around all three axes. Then we join the original crystal 1 with its rotated brother.
Of course, the two parts will not fit, so we remove or fill in matter as required.
So how many numbers do you need to describe what we just did? How many numbers are needed to describe the basic geometry of a planar grain boundary?
Grain boundary geometry
The formal production of a grain boundary
Let's make it short: We need 5 numbers to describe what we did: Three number (=rotation angles, for example) to describe the relative rotation of the grains to each other, and two numbers to describe the position of the grain boundary plane.
One is inclined to think hat one needs three numbers for determining the exact position of the grain boundary plane too, since a normal vector perpendicular on this plane (the red vector in the drawing above) has three components. Yes, but a normal vector has a defined magnitude and we don't care for that. The length on the vector characterizing the grain boundary plane is unimportant, and that means that two numbers will do.
What we want to know about a grain boundary is its atomic structure and, related to that, its energy EGB (per cm2, of course). We have a formidable task ahead, because the quantities we are after are functions of at least 5 variables! And that's only for the simple problem of a planar boundary. If the grain boundary is curved, which it needs to be to enclose a grain, the two parameters characterizing the grain boundary plane, become functions of the position.
Why do we want to know the grain boundary energy? Because the basic question we have is:

Are there special grain boundaries with
particular low energies?

If there are, we might expect that crystals go for them; they want to minimize their (free) energy after all.
You might think that the question is moot, because as soon as the first small crystallites form at some nuclei, their orientation is given. When those crystallites grow together, the relative orientation of the grains is what it is. Nothing the crystal can do about it.
You are almost right. The relative orientation of the grains is indeed whatever it is. But the crystal, being much smarter than you as far as grain boundaries (and possibly a few other things) are concerned, still knows a trick or two about minimizing energy.
  Minimizing Energy With Respect to the Grain Boundary Plane
Let's start assuming that the orientation relation between the two grains is given. The actual grain boundary still could be on any plane with respect to some coordinate system, for example the Bravais lattice of grain 1. The specific and simpler question is now: Are there any special low-energy planes for the given orientation?
You bet there are. Not that I can demonstrate this for any orientation and any plane, but one example is enough to get the gist of the argument across.
Grain boundary plane optimization Grain boundary plane optimization
Possible Boundary planes in a "diamond twin"
We are looking at a very special orientation between two grains of a crystal, called "twin" orientation. We have a diamond-structure, but twins work for any lattice: one grain is simply the mirror image of the other one. Two grain boundary planes are shown and it is ridiculously obvious that the one on the right is far, far "better", meaning it has a far lower energy then the one on the left.
On the right, all atoms find partners at the proper distance and can bond happily. On the left, you can't even draw what is going to happen. A lot of atoms around this boundary plane will be very unhappy.
It is clear that something like this happens for any grain orientation relationship, and that there are always some special planes with lower energy than the rest. So what is the crystal going to do about this?
It will break up the boundary plane into properly oriented facets as shown here.
Facetting of grain boundaries
Facetting of Grain Boundary Planes to Lower the Energy
All the crystal needs to do is to move a few atoms close to the boundary a little bit. This is not difficult at high temperatures, when atoms are mobile.
We might safely assume that grain boundaries will be facetted into low energy planes. What kind of planes that are for some arbitrary orientation is not so easy to predict, however. Nevertheless, facetting will happen. It might be on a scale so small that we don't see it easily but it will be there. No more needs to be said about this topic.
  Interlude: Making Low Angle Grain Boundaries with Dislocations
Let's make the most simple grain boundary imaginable by using the recipe from above. What we do then is to cut the crystal in twain and rotate the upper part. To do that as simply as possible, we rotate only around one axis and keep the rotation angle small.
There are two basic ways of doing this, called "twist" and "tilt". When you make a twist boundary, the axis of rotation is in the plane of the cut and the future grain boundary, if you make a tilt boundary, the axis of rotation is at right angles to the plane of the cut and the future grain boundary. An arbitrary boundary can then be made by combining twist and tilt.
The figures below illustrate that. They also show that you can make one and the same boundary in two ways, at least as far as the "twin boundary" in a diamond crystal is concerned that is shown once more below. That doesn't prove that you can do that for all possible boundaries but makes clear that there could be some complications with this recipe. Rest assured that there are! And that you really do not want to learn more about it.
Twist grain boundary
Making the same diamond twin boundary in two ways, using either "twist" or "tilt"
Here I only want to show that you can make so-called "small-angle" grain boundaries of all kinds by combining the two special periodic dislocation arrangements that we get for either a pure tilt or a pure twist small-angle grain boundary.
What is a small-angle grain boundary? Any boundary where you twist or tilt only by a few degrees, so that the two grains have almost the same orientation.
Here is the way it's done:
Small angle tilt boundary in silicon
Pure tilt small angle grain boundary; principle and the real thing
Small angle twist boundary in silicon
Pure twist boundary; principle and the real thing
Source: The drawing in the lower left goes back, I believe, to Read .The other pictures are mine.
Contrasted are schematic drawings and a HRTEM images of the real thing. In the lower picture, just one set of screw dislocation is visible in the HRTEM image by the shift induced in the lattice planes above the grain boundary plane.
Refer to the "science of dislocation" module for general information and in particular to the screw dislocation stuff
The way a tilt boundary "works" by employing edge dislocations is obvious. You just need a parallel array of dislocation spaced at some distance that determines the tilt angle. For a twist boundary you need a network of screw dislocations. It could be square as shown above or here, or hexagonal and complicated as in this picture.
Of course, this simple approach only works for small misorientation angles of at most a few degrees; too large an angle, and the dislocations have to get so close that it doesn't make sense anymore.
Mix the two kinds of dislocation arrangements, and you get rather complex but well-defined and understood dislocation structures for any small-angle grain boundary with some twist and some tilt.
This is complicated but the important thing to realize is why the crystal is actually doing all this. It introduces dislocations for one reason only. All the mismatch caused by having grains with different orientations is downloaded into just the core of the dislocations. In between the dislocations the match of the two lattices is perfect.
In other words: The crystal prefers to have a large pain concentrated in a small area with large painless regions in between to a large area with medium pain everywhere. Who wouldn't. Going shopping with your wife in a major way once in a while is by far preferable to a bit of shopping all the time.
That will also be the guiding principle for what to do in arbitrary large-angle grain boundary.
  Structure of Arbitrary Grain Boundaries
There are infinitely many ways you can lie in bed. On your back, on your side, legs pulled up or down, and so on. But a few well-defined positions are just a lot more comfy that all the others. There are infinitely many ways you can orient a grain with respect to the other. But a few well-defined orientations just have a lower energy than all the others.
The crystal knows what those particular comfy "low sigma" orientations are: orientations where right at the grain boundary as many atoms as possible have the same position in grain 1 and in grain 2. And no, it doesn't matter where exactly the grain boundary is positioned; the crystal can always make itself comfortable in this respect by facetting.
It is easy to get an idea about these special orientations. Look at the animation below. We make a twist boundary but we won't stop at small angles..
What you see is that at certain angles there is a perfect match of lattice points. Put atoms there and they have the same position in both grains.
This can be generalized for general lattices and three dimensions; note that I emphatically do not say "easily generalized". Just let two three-dimensional lattices interpenetrate and rotate one in all directions. Calculating the lattice of coinciding points or the so-called O-lattice, a name forever associated with W. Bollmann, is not something lightly undertaken with just some high school math. And that's just the comparatively simple beginning of calculating what kind of tricky structure the crystal will now put up if it finds itself close to, but not exactly in, some preferred "low sigma" orientation.
So what does that "low sigma" mean? Well, if there is some coincidence between points of the two lattices, those points define a lattice, too. The volume of an elementary cell of this "coincidence site lattice" or CSL, divided by the volume of the elementary cell of the crystal lattice, will always be an odd integer that is given the assignation sigma or S. Our old friend, the twin boundary, now carries the assignation S3 boundary.
Here are drawings (of course only in 2 dimensions) of the S3 or twin boundary and a S5 boundary, the next best thing.
Coincidence site lattices (CSL)
Interpenetrating cubic lattices producing a
S3 and a S5 CSL or "Coincidence Site Lattice"
But let's not go into details, e.g. why only odd-numbered sigma values exist, but draw a simple conclusion:

There are special low-energy orientations.
The crystal will do something if it finds
one of its grain boundaries close to
such an orientation.

What the crystal will do is to generate a dislocation arrangement that produces a small-angle grain boundary in such a way that the additional "small angle" added to the basic large angle defining the boundary, will orient the grain boundary in the exact low-energy and typically low-sigma orientation.
It's the old principle. Invest some energy into the making of a dislocation network, to gain a lot of energy because you now have a low-energy boundary.
There is a catch to this, however. The dislocation arrangement that by itself would define a low-angle grain boundary needs to sit right in the actual large-angle boundary since it must belong to both grains. But how do you define a dislocation in two lattices that are not connected in a continuous way?
You don't because you can't. That's why grain boundary dislocations are defined in a new lattice, a lattice that is common to both grains. The coincidence site lattice is common to both grains, so we could take that lattice and make a dislocations by the standard "cut-and-shift" procedure. You would make monster dislocations in this way, because you need to shift a large amount since the CSL lattice is always much larger than the lattices of the crystals. Dislocations in the CSL lattice would have large Burgers vectors, in other words. If you would do that (and I leave open how you would do that in a real grain boundary in a real crystal and not just on a piece of paper), you would be in for a surprise. Your monster dislocations would split into a bunch of "small" dislocations with small Burgers vectors. Those are what we call "grain boundary dislocations".
They can do this because if you look closely at the geometry once more, you recognize that there is another lattice common to both crystals with unit vectors smaller than the actual crystal lattice. It is called the "DSC" lattice for "displacement shift complete". Not the best of all possible names, but that's what it is called. Just for the hell of it, I show you two of these dislocations (edge type) in a S5 boundary:
Grain boundary dislocations in DSC lattice
Grain boundary dislocation
Grain boundary dislocation in a S5 boundary
The red points belong to lattice 1, the green ones to lattice 2. The blue ones are common in both lattices and thus define the coincidence site lattice. The black lines constitute the DSC lattice; here it is simply the lattice common to all lattice points. A cut (blue or pink line) combined with a shift (red vector) produces an (edge) dislocation in the DSC lattice. This dislocation moves the boundary as shown, the yellow "structure units" illustrate that.
Imagine a regular array of these dislocations, and you have a small angle boundary superimposed on the S5 boundary. If the real boundary would have been off the S5 orientations by a small angle, it now would be turned into the precise S5 orientation.
All crystals do that all the time. They have no problem in figuring out the best way to restructure their boundaries in the way described above. And that's why we see all these "grain boundary dislocations" all the time in our electron microscopes.
We know why these dislocations are there in principle. However, if we want to calculate the details, it gets hellishly difficult. Be happy that I won't go into how it is done.

© H. Föll

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