## Nucleation Science |

## 2. Homogeneous Nucleation | |||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||

In the preceding module we have looked at a constant
but supersaturated concentration of vacancies or impurity atoms. That taught us a few important things that we are going
to need here - but the whole approach was unrealistic. The crystal, after all, wants to get rid of the supersaturation and
that involves that the concentration comes down. We need to make a "big" precipitate with lots of point defects
in it, not just tiny clusters.As in the preceding module, we assume a crystal that is absolutely perfect except for some supersaturated point defects. The crystal has to do whatever needs to be done all by itself, in particular it must make the nuclei required to start precipitation without external or extrinsic "help". It would thus be logical to call that process "
intrinsic" nucleation. I won't, however, because it has always been called "homogeneous
nucleation" for historical reasons. Since this is also a good term, let's go with the flow here. |
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Let's assume that the precipitate is spherical, with a diameter of .
The basic problem in making precipitates is simple:r- Putting atoms
*inside*the precipitate leads to a*gain*in energy. This is good. - The interface precipitate - matrix has some interface energy. If the precipitate grows because we keep putting atoms
inside, the interface area increases. This
*costs*energy and that is bad.
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To get a feeling of what is involved, let's look at some numbers. We have the following relations
for the surface area and the volume S of the spheres, the number V of atoms
or vacancies contained in the sphere, the number No. V of atoms or vacancies sitting on the surface of the
sphere, and the ratio between atoms in the bulk and on the surface in percent. No. S | |||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||

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Of course, clusters smaller than 8, 9, or 12 atoms for bcc, prim. cubic or fcc crystals, respectively, have all of their atoms or vacancies at the "surface". | |||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||

What we see very clearly is that the energy gained by putting atomic defects into
"prison" is pretty much lost again by having most atoms or vacancies at the surface for very
small clusters or the nuclei of precipitates. Only for clusters larger than
10 nm or so, the volume will win. | |||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||

We knew that all along. "You get more potato peel from 20 small potatoes than from
one big one!" is stated in the backbone right
about here.True enough. But now we will calculate exactly how much more potato
peel we are talking here. | |||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||

Essentially, whenever we consider to produce a precipitate with radius
by agglomerating particles like impurity atoms, vacancies, interstitials or any mix thereof, we need to figure out if the
balance rD of the energies involved makes the investment worthwhile.
Only if the making of a precipitate offers a solid chance for G(r)decreasing the free energy
of a crystal with a supersaturation of something, the investment would make sense. Note that I'm not saying
that there must be an Gimmediate or direct return on investment! We have only two energy terms to consider: - The
**surface energy**that we have to invest for making a precipitate with a certain surface, or better interface area.*E*_{S}is quite simply given by the area*E*_{S}**4p**of the surface, times the specific interface energy*r*^{2}**g**of the interface in question. Its sign is always positive; we have to "pay". - The (free) energy gained by imprisoning one surplus particle in the precipitate. This energy is given by the volume
**4/3(p**of the precipitate times the energy*r*^{3})**D**gained per particle volume. Its sign is negative since we gain energy.*g*
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The energy balance thus quite simply writes | |||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||

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This is a simple function of the type y = ax^{2} –
bx^{3}
a and b you enter, the general behavior is always as shown below for
the most simple case. In other words, our curve looks exactly the same - just change the
scales to G(r) and G and provide the right numbers on the scales. With increasing radius r, starting from
r, the energy balance always increases, reaches a maximum, and then decreases,
eventually becoming negative as desired.r = 0 nm | |||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||

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What can we learn form this? Two things:
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1. There is a critical radius
for a viable nucleus, given by the r_{ crit}maximum of the
curve. A nucleus (or tiny precipitate) with this size will G(r)not yet have provided a lower
free energy for the crystal but will produce a net return if it grows beyond that critical size. It then will tend to grow. Precipitates smaller than the critical radius would tend to shrink.
The critical size is easy to calculate from setting the differential quotient dG(r)/dr
= 0 | |||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||

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2. I derived that result for the clustering of something like vacancies
or impurity atoms inside a solid crystal. Let's now look at the solidification of a liquid. Look, or even better, think. Did you get it? | |||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||

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When a liquid solidifies, you need to start somewhere to put the atoms together
in crystalline form. There is some energy gain for temperatures below the melting point if atoms are put into the system,
and there is some solid - liquid interface with some interface energy g. Same thing as
before. Just the numbers for g
and D are different.gYou do all the other examples. | |||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||

Actually, looking at freezing offers a little bonus: We know something about D ! We know that in order to melt a certain amount of a solid, you must invest a defined
amount of energy. When the liquid solidifies, you get exactly that energy back. It is called the "gheat of fusion" , and is rather easy to determine. In contrast, the H_{F}D from above, describing properties of particles like vacancies
or impurity atoms and their temperature dependence is not all that easy to get.g | |||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||

For the critical radius of a nuclei for solidification
we get: | |||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||

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We have H_{F} · (T_{ M} – T)/T_{M}D. gThe quantity , i.e.
the difference between the melting point temperature and the actual temperature at which the material is still liquid, is
called "T_{M} – Tsupercooling" or undercooling. Supercooling
and supersaturation are closely related; they simply describe how much a system deviates from equilibrium. | |||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||

The critical radius scales directly with the interface energy g.
The interface energy is pretty much a constant, independent of temperature or supersaturation, and thus easy to assess.The critical radius scales inversely with the energy D that is to gain, and we
if we generalize a bit, with the supersaturation / supercooling. gSo the critical radius does decrease for small interface energies, large energy gains, and with increasing supersaturation. That makes sense. | |||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||

But let's not dawdle any more. Let's look at numbers for critical radii. There
is, of course, a large spread of possible g, and H_{F}
D values for whatever possible process, supercooling or supersaturation
you look at, but no matter:g | |||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||

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What does "far too large" mean?
Well, let's first consider what we could have in terms of small nuclei. We did that already in the "Global and Local Equilibrium for Point Defects" module. | |||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||

We might get a very few clusters with more than 5 or 6 vacancies / impurity atoms
in it, but that will be clusters with nominal radii well below 1 nm. And we need much more
for most cases - 5 nm or 10 nm! Nuclei with such a critical radius carry far more energy
around than a typical vacancy or impurity atom, and the probability for having clusters or nuclei with such a high energy
is given by the ubiquitous Boltzmann factor
E_{n}exp- - and is zero for all practical concerns!E_{n}/kT | |||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||

What that means is simple: | |||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||

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Well, almost never. Solidification, for example, would
require undercoolings of up to 100 K before the critical radii required are small enough to initiate freezing, and that's
just not what we observe. Typically, undercoolings of at most a few degrees will do the trick. Only ultra-clean liquids
under tightly controlled laboratory conditions can be supercooled to a large extent, i.e. stay liquid well below their freezing
point. | |||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||

Where does that leave us? Well - obviously there is another, more efficient nucleation
mechanisms. Yes, there is! It is called heterogeneous nucleation (surprise!), and it
utilizes defects. | |||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||

That will be the topic of the next module in this series. | |||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||

Back to | ||

Nucleation Science Overview | ||

1. Global and local equilibrium for point defects |
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On to | ||

3. Heterogeneous nucleation |
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4. Size and density of precipitates |
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5. Precipitation and structures |
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8.2.2 It's a Long way to Nirvana

TTT Diagrams: 1. The Basic Idea

Experimental Techniques for Measuring Diffusion Parameters

Size and Density of Precipitates

Intrinsic Gettering in Silicon

Global and Local Equilibrium for Point Defects

Constitutional Supercooling and Interface Stability

TTT Diagrams 4. Experimental Construction of TTT and Phase Diagrams

© H. Föll (Iron, Steel and Swords script)