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Commit e1e7fd65 authored by Nicolas Eßing's avatar Nicolas Eßing
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Tex on nucleation theory fit, some notes and fixes

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......@@ -16,7 +16,7 @@ plt.rcParams.update({'font.size': 16,
# As their layer was really thin, assume 2D theories
dimensions = 2;
dimensions = 2
# Literature values for melting temperature, latent heat and interfacial energy
# Taken from AIST
......@@ -129,8 +129,8 @@ def nucleationratefit(plotrange=None, show=True):
absolute_sigma=True)
# p0=[b0,Literature.IE,Literature.L,Literature.Tm]
if show:
print("Fitting J = b*dGv**2/(8*pi)/sqrt(IE**3*kB*T) * exp(-dGc/kB/T)")
print(" dGc = 16*pi*IE^3/(3*dGv)")
print("Fitting J = b*dGv^2/(8*pi)/sqrt(IE^3*kB*T) * exp(-dGc/kB/T)")
print(" dGc = 16*pi*IE^3/(3*dGv^2)")
print(" dGv = L*(Tm-T)/Tm*2*T/(Tm+T)")
print("b: ",popt[0],"+-",np.sqrt(pcov[0,0]))
print("IE:",popt[1],"+-",np.sqrt(pcov[1,1]))
......
......@@ -89,7 +89,7 @@ materials as well.
For late times however, as $f_a$ and $\Delta N$ get small,
the fluctuations can get greater then the mean value,
which makes it dificult to see if the rate is not constant.
It can be made easyer by integrating the rate again.
It can be made easier by integrating the rate again.
This gives a number of nuclei corrected by the effect of the shrinking
volume free to nucleation and is called $N_{\text{corrected}}$ here.
......@@ -194,19 +194,20 @@ materials as well.
\label{fig:expfit_jmak_comp}
\end{figure}
\section{Temperature Dependence of Groth Velocity}
\section{Temperature Dependence of Growth Velocity}
The estimated growth velocities for different temperatures can be described by
one temperature dependent model.
With only four data points available,
an Arrhenius model can sufficiently describe the behaviour. % chisq/ndf of 3.0
This can be seen in figure \ref{fig:expfit_v_arrhenius}.
Collectively, for the growth velocity
Collectively, the growth velocity
\begin{align}
% v &= (1.9 \pm 3.0) \exp(-\frac{(21123 \pm 617)\unit{K}}{T}) \\
v &= (1.9 \pm 3.0) \exp(-\frac{(1.82 \pm 0.05)\unit{eV}}{k_B T})
v &= (1.9 \pm 3.0) \frac{\text{m}}{\text{s}} \cdot
\exp\left(-\frac{(1.82 \pm 0.05)\unit{eV}}{k_B T}\right)
\end{align}
should be useable for \sbte in this temperature range and vicinity.
should be useable for \sbte{} in this temperature range and vicinity.
\begin{figure}[ht]
\begin{subfigure}{.49\linewidth}
......@@ -226,7 +227,41 @@ materials as well.
Fitting an Arrhenius behaviour to the mobility gives less consistent results.
\section{Classical Nucleation Theory}
%TODO
Estimation of $\gamma$, possibly more
In the data, the nucleation rates are not constant over time,
an effect not described by the introduced classical nucleation theory.
The time dependence of the rates are not similar for the different
measurements, which makes it especially complex to find a general model.
To get a simple model providing values for the rate for other temperatures,
the mean rates of each measurement can be used.
The classical nucleation theory model was fitted to this data.
For $\dGv$, the introduced model was used
together with values from other experiments \citep{expdata,sb2teStructure}:
\begin{align}
T_m &\approx 837.5 \unit{K} \\
L &= 47.2 \, \frac{\text{J}}{\text{g}} \cdot 6.28 \, \frac{\text{g}}{\text{cm}^3} \\
&= 296.4 \cdot 10^6 \, \frac{\text{J}}{\text{m}^3}
\end{align}
This leaves the prefactor and the interfacial energy as free parameters.
With more than 4 measurements it should also be possible to fit with more than
two free parameters.
As the rates are not constant, this will probably not improve quality of the
results significant.
\begin{figure}[h]
\centering
\includegraphics[width=.5\linewidth]{../img/expfit_J_T.png}
\caption{Classical nucleation theory fit onto experiment data on \sbte.
Here a rate per area is used, as the thickness was the same.}
\label{fig:expfit_cnt}
\end{figure}
The resulting values of
\begin{align}
\beta &= (8.3 \pm 34.0) \cdot 10^{80} \unit{s}^{-1} \\
\gamma &= (89.52 \pm 0.56) \frac{\text{mJ}}{\text{m}^2}
\end{align}
% correlation of 0.999986
have quite large uncertainties, but should be useable as an initial guess.
The fit is shown in figure \ref{fig:expfit_cnt}.
......@@ -90,7 +90,8 @@ and simple simulations to test the limits of the calculated behaviour.
A ``branch to composition'' technique \citep{computerOrganizations} was used
to avoid expensive branching operations.
Overall, the new implementation needs about $9\%$ the time of the old one.
Overall, the new implementation needs about $9\%$ the time of the old one
and should thus shorten the runtime by more than $20\%$.
\subsection{Other Improvements and Performance Summary}
Apart from the discussed changes, some minor improvements were made. \\
......
......@@ -336,10 +336,6 @@ abstract = { ▪ Abstract The phase-field method has recently emerged as a pow
publisher={ACS Publications}
}
theory_of_mixtures-lecture-notes.pdf
Theory lectures how to come to phase field equations from a physical point,
not so ad-hoc like zhiyang
On the performance lost from if statements (and also the technique I am using now)
@article{computerOrganizations,
title={Some computer organizations and their effectiveness},
......@@ -351,3 +347,16 @@ On the performance lost from if statements (and also the technique I am using no
year={1972},
publisher={IEEE}
}
% Some properties of Sb2Te, not much, but at least a density
% I read the given URL, which quotes this paper
@article{sb2teStructure,
author = "Agafonov, V. and Rodier, N. and Ceolin, R. and Bellissent, R. and Bergman, C. and Gaspard, J.P.",
title = "Structure of Sb2Te",
journal = "Acta Crystallographica, Section C: Crystal Structure Communications",
year = "1991",
volume = "47",
pages = "1141-1143",
ASTM_id = "ACSCEE",
url = "https://materialsproject.org/materials/mp-6997/"
}
......@@ -71,12 +71,16 @@ the phase field model.
and a jump distance \citep{NucleationTheory}.
Alternatively, it can be used as a free parameter when
fitting this equation onto experimental data.
% As the actual rates differ from the calculated up to some orders of
% magnitude \citep{balluffi}, this might be a better approach.
Alltogether, one gets
\begin{align}
J &= \beta \frac{Z}{V_m} e^{\frac{-\Delta G_c}{k_B T}} \\
&= \frac{3 \beta}{4 \pi r_c^3} \sqrt{\frac{\Delta G_c}{3 \pi k_B T}}
e^{\frac{-\Delta G_c}{k_B T}} \ ,
% &= \frac{\beta \dGv^2}{8 \pi} \sqrt{\frac{1}{\gamma^3 k_B T}}
% e^{\frac{-16 \pi \gamma^3}{3 \dGv^2 k_B T}}
\label{eq:cnt_J}
\end{align}
where $V_m$ is the volume of a monomer
......@@ -238,11 +242,22 @@ the phase field model.
This equation has been used for phase change materials by several authors
\citep{CrystallizationKinetics, SbTeArrhenius, AistExperiments, crystalGrowthInPcm}.
\subsection{Interafcial Energy}
At the interface between two phases, energetically higher structures
exist to fit the two structures together. %TODO citation
This energy per unit of interfacial area is called
interfacial energy $\gamma$.
It plays a role in the classical nucleation theory as the energy barrier
for the formation of a new grain.
Its ratio to the bulk free energy defines the critical radius.
From a fit to the equation from this theory, a value can be estimated,
which is one way to determine this parameter \citep{SbTeArrhenius}.
It is also responsible for the Gibbs-Thomson effect and can be determined
from measurements of this. %TODO citation, equation, ...
%TODO other physical quantities?
% \subsection{Interfacial Energy}
% ratio to bulk free energy defines critical radius of nucleation
% can be measured in Gibbs-Thomson effect
% or fitted from CNT
\subsection{Crystallized Fraction}
The main quantity of interest is the fraction $f_c$ of the material that
......
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