45 |
|
|
46 |
|
\begin{abstract} |
47 |
|
|
48 |
< |
We have developed a Non-Isotropic Velocity Scaling algorithm for |
49 |
< |
setting up and maintaining stable thermal gradients in non-equilibrium |
50 |
< |
molecular dynamics simulations. This approach effectively imposes |
51 |
< |
unphysical thermal flux even between particles of different |
52 |
< |
identities, conserves linear momentum and kinetic energy, and |
53 |
< |
minimally perturbs the velocity profile of a system when compared with |
54 |
< |
previous RNEMD methods. We have used this method to simulate thermal |
55 |
< |
conductance at metal / organic solvent interfaces both with and |
56 |
< |
without the presence of thiol-based capping agents. We obtained |
57 |
< |
values comparable with experimental values, and observed significant |
58 |
< |
conductance enhancement with the presence of capping agents. Computed |
59 |
< |
power spectra indicate the acoustic impedance mismatch between metal |
60 |
< |
and liquid phase is greatly reduced by the capping agents and thus |
61 |
< |
leads to higher interfacial thermal transfer efficiency. |
48 |
> |
With the Non-Isotropic Velocity Scaling algorithm (NIVS) we have |
49 |
> |
developed, an unphysical thermal flux can be effectively set up even |
50 |
> |
for non-homogeneous systems like interfaces in non-equilibrium |
51 |
> |
molecular dynamics simulations. In this work, this algorithm is |
52 |
> |
applied for simulating thermal conductance at metal / organic solvent |
53 |
> |
interfaces with various coverages of butanethiol capping |
54 |
> |
agents. Different solvents and force field models were tested. Our |
55 |
> |
results suggest that the United-Atom models are able to provide an |
56 |
> |
estimate of the interfacial thermal conductivity comparable to |
57 |
> |
experiments in our simulations with satisfactory computational |
58 |
> |
efficiency. From our results, the acoustic impedance mismatch between |
59 |
> |
metal and liquid phase is effectively reduced by the capping |
60 |
> |
agents, and thus leads to interfacial thermal conductance |
61 |
> |
enhancement. Furthermore, this effect is closely related to the |
62 |
> |
capping agent coverage on the metal surfaces and the type of solvent |
63 |
> |
molecules, and is affected by the models used in the simulations. |
64 |
|
|
65 |
|
\end{abstract} |
66 |
|
|
73 |
|
%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%% |
74 |
|
|
75 |
|
\section{Introduction} |
74 |
– |
[BACKGROUND FOR INTERFACIAL THERMAL CONDUCTANCE PROBLEM] |
76 |
|
Interfacial thermal conductance is extensively studied both |
77 |
< |
experimentally and computationally, and systems with interfaces |
78 |
< |
present are generally heterogeneous. Although interfaces are commonly |
79 |
< |
barriers to heat transfer, it has been |
80 |
< |
reported\cite{doi:10.1021/la904855s} that under specific circustances, |
81 |
< |
e.g. with certain capping agents present on the surface, interfacial |
82 |
< |
conductance can be significantly enhanced. However, heat conductance |
83 |
< |
of molecular and nano-scale interfaces will be affected by the |
84 |
< |
chemical details of the surface and is challenging to |
85 |
< |
experimentalist. The lower thermal flux through interfaces is even |
85 |
< |
more difficult to measure with EMD and forward NEMD simulation |
86 |
< |
methods. Therefore, developing good simulation methods will be |
87 |
< |
desirable in order to investigate thermal transport across interfaces. |
77 |
> |
experimentally and computationally\cite{cahill:793}, due to its |
78 |
> |
importance in nanoscale science and technology. Reliability of |
79 |
> |
nanoscale devices depends on their thermal transport |
80 |
> |
properties. Unlike bulk homogeneous materials, nanoscale materials |
81 |
> |
features significant presence of interfaces, and these interfaces |
82 |
> |
could dominate the heat transfer behavior of these |
83 |
> |
materials. Furthermore, these materials are generally heterogeneous, |
84 |
> |
which challenges traditional research methods for homogeneous |
85 |
> |
systems. |
86 |
|
|
87 |
+ |
Heat conductance of molecular and nano-scale interfaces will be |
88 |
+ |
affected by the chemical details of the surface. Experimentally, |
89 |
+ |
various interfaces have been investigated for their thermal |
90 |
+ |
conductance properties. Wang {\it et al.} studied heat transport |
91 |
+ |
through long-chain hydrocarbon monolayers on gold substrate at |
92 |
+ |
individual molecular level\cite{Wang10082007}; Schmidt {\it et al.} |
93 |
+ |
studied the role of CTAB on thermal transport between gold nanorods |
94 |
+ |
and solvent\cite{doi:10.1021/jp8051888}; Juv\'e {\it et al.} studied |
95 |
+ |
the cooling dynamics, which is controlled by thermal interface |
96 |
+ |
resistence of glass-embedded metal |
97 |
+ |
nanoparticles\cite{PhysRevB.80.195406}. Although interfaces are |
98 |
+ |
commonly barriers for heat transport, Alper {\it et al.} suggested |
99 |
+ |
that specific ligands (capping agents) could completely eliminate this |
100 |
+ |
barrier ($G\rightarrow\infty$)\cite{doi:10.1021/la904855s}. |
101 |
+ |
|
102 |
+ |
Theoretical and computational models have also been used to study the |
103 |
+ |
interfacial thermal transport in order to gain an understanding of |
104 |
+ |
this phenomena at the molecular level. Recently, Hase and coworkers |
105 |
+ |
employed Non-Equilibrium Molecular Dynamics (NEMD) simulations to |
106 |
+ |
study thermal transport from hot Au(111) substrate to a self-assembled |
107 |
+ |
monolayer of alkylthiolate with relatively long chain (8-20 carbon |
108 |
+ |
atoms)\cite{hase:2010,hase:2011}. However, ensemble averaged |
109 |
+ |
measurements for heat conductance of interfaces between the capping |
110 |
+ |
monolayer on Au and a solvent phase has yet to be studied. |
111 |
+ |
The relatively low thermal flux through interfaces is |
112 |
+ |
difficult to measure with Equilibrium MD or forward NEMD simulation |
113 |
+ |
methods. Therefore, the Reverse NEMD (RNEMD) methods would have the |
114 |
+ |
advantage of having this difficult to measure flux known when studying |
115 |
+ |
the thermal transport across interfaces, given that the simulation |
116 |
+ |
methods being able to effectively apply an unphysical flux in |
117 |
+ |
non-homogeneous systems. |
118 |
+ |
|
119 |
|
Recently, we have developed the Non-Isotropic Velocity Scaling (NIVS) |
120 |
|
algorithm for RNEMD simulations\cite{kuang:164101}. This algorithm |
121 |
|
retains the desirable features of RNEMD (conservation of linear |
122 |
|
momentum and total energy, compatibility with periodic boundary |
123 |
|
conditions) while establishing true thermal distributions in each of |
124 |
< |
the two slabs. Furthermore, it allows more effective thermal exchange |
125 |
< |
between particles of different identities, and thus enables extensive |
126 |
< |
study of interfacial conductance. |
124 |
> |
the two slabs. Furthermore, it allows effective thermal exchange |
125 |
> |
between particles of different identities, and thus makes the study of |
126 |
> |
interfacial conductance much simpler. |
127 |
|
|
128 |
+ |
The work presented here deals with the Au(111) surface covered to |
129 |
+ |
varying degrees by butanethiol, a capping agent with short carbon |
130 |
+ |
chain, and solvated with organic solvents of different molecular |
131 |
+ |
properties. Different models were used for both the capping agent and |
132 |
+ |
the solvent force field parameters. Using the NIVS algorithm, the |
133 |
+ |
thermal transport across these interfaces was studied and the |
134 |
+ |
underlying mechanism for this phenomena was investigated. |
135 |
+ |
|
136 |
+ |
[MAY ADD WHY STUDY AU-THIOL SURFACE; CITE SHAOYI JIANG] |
137 |
+ |
|
138 |
|
\section{Methodology} |
139 |
< |
\subsection{Algorithm} |
140 |
< |
[BACKGROUND FOR MD METHODS] |
141 |
< |
There have been many algorithms for computing thermal conductivity |
142 |
< |
using molecular dynamics simulations. However, interfacial conductance |
143 |
< |
is at least an order of magnitude smaller. This would make the |
144 |
< |
calculation even more difficult for those slowly-converging |
145 |
< |
equilibrium methods. Imposed-flux non-equilibrium |
139 |
> |
\subsection{Imposd-Flux Methods in MD Simulations} |
140 |
> |
For systems with low interfacial conductivity one must have a method |
141 |
> |
capable of generating relatively small fluxes, compared to those |
142 |
> |
required for bulk conductivity. This requirement makes the calculation |
143 |
> |
even more difficult for those slowly-converging equilibrium |
144 |
> |
methods\cite{Viscardy:2007lq}. |
145 |
> |
Forward methods impose gradient, but in interfacail conditions it is |
146 |
> |
not clear what behavior to impose at the boundary... |
147 |
> |
Imposed-flux reverse non-equilibrium |
148 |
|
methods\cite{MullerPlathe:1997xw} have the flux set {\it a priori} and |
149 |
< |
the response of temperature or momentum gradients are easier to |
150 |
< |
measure than the flux, if unknown, and thus, is a preferable way to |
151 |
< |
the forward NEMD methods. Although the momentum swapping approach for |
152 |
< |
flux-imposing can be used for exchanging energy between particles of |
153 |
< |
different identity, the kinetic energy transfer efficiency is affected |
154 |
< |
by the mass difference between the particles, which limits its |
113 |
< |
application on heterogeneous interfacial systems. |
149 |
> |
the thermal response becomes easier to |
150 |
> |
measure than the flux. Although M\"{u}ller-Plathe's original momentum |
151 |
> |
swapping approach can be used for exchanging energy between particles |
152 |
> |
of different identity, the kinetic energy transfer efficiency is |
153 |
> |
affected by the mass difference between the particles, which limits |
154 |
> |
its application on heterogeneous interfacial systems. |
155 |
|
|
156 |
< |
The non-isotropic velocity scaling (NIVS)\cite{kuang:164101} approach in |
157 |
< |
non-equilibrium MD simulations is able to impose relatively large |
158 |
< |
kinetic energy flux without obvious perturbation to the velocity |
159 |
< |
distribution of the simulated systems. Furthermore, this approach has |
156 |
> |
The non-isotropic velocity scaling (NIVS)\cite{kuang:164101} approach to |
157 |
> |
non-equilibrium MD simulations is able to impose a wide range of |
158 |
> |
kinetic energy fluxes without obvious perturbation to the velocity |
159 |
> |
distributions of the simulated systems. Furthermore, this approach has |
160 |
|
the advantage in heterogeneous interfaces in that kinetic energy flux |
161 |
|
can be applied between regions of particles of arbitary identity, and |
162 |
< |
the flux quantity is not restricted by particle mass difference. |
162 |
> |
the flux will not be restricted by difference in particle mass. |
163 |
|
|
164 |
|
The NIVS algorithm scales the velocity vectors in two separate regions |
165 |
|
of a simulation system with respective diagonal scaling matricies. To |
166 |
|
determine these scaling factors in the matricies, a set of equations |
167 |
|
including linear momentum conservation and kinetic energy conservation |
168 |
< |
constraints and target momentum/energy flux satisfaction is |
169 |
< |
solved. With the scaling operation applied to the system in a set |
170 |
< |
frequency, corresponding momentum/temperature gradients can be built, |
171 |
< |
which can be used for computing transportation properties and other |
172 |
< |
applications related to momentum/temperature gradients. The NIVS |
132 |
< |
algorithm conserves momenta and energy and does not depend on an |
133 |
< |
external thermostat. |
168 |
> |
constraints and target energy flux satisfaction is solved. With the |
169 |
> |
scaling operation applied to the system in a set frequency, bulk |
170 |
> |
temperature gradients can be easily established, and these can be used |
171 |
> |
for computing thermal conductivities. The NIVS algorithm conserves |
172 |
> |
momenta and energy and does not depend on an external thermostat. |
173 |
|
|
174 |
|
\subsection{Defining Interfacial Thermal Conductivity $G$} |
175 |
|
For interfaces with a relatively low interfacial conductance, the bulk |
187 |
|
T_\mathrm{cold}\rangle}$ are the average observed temperature of the |
188 |
|
two separated phases. |
189 |
|
|
190 |
< |
When the interfacial conductance is {\it not} small, two ways can be |
191 |
< |
used to define $G$. |
190 |
> |
When the interfacial conductance is {\it not} small, there are two |
191 |
> |
ways to define $G$. |
192 |
|
|
193 |
< |
One way is to assume the temperature is discretely different on two |
194 |
< |
sides of the interface, $G$ can be calculated with the thermal flux |
195 |
< |
applied $J$ and the maximum temperature difference measured along the |
196 |
< |
thermal gradient max($\Delta T$), which occurs at the interface, as: |
193 |
> |
One way is to assume the temperature is discrete on the two sides of |
194 |
> |
the interface. $G$ can be calculated using the applied thermal flux |
195 |
> |
$J$ and the maximum temperature difference measured along the thermal |
196 |
> |
gradient max($\Delta T$), which occurs at the Gibbs deviding surface, |
197 |
> |
as: |
198 |
|
\begin{equation} |
199 |
|
G=\frac{J}{\Delta T} |
200 |
|
\label{discreteG} |
215 |
|
|
216 |
|
With the temperature profile obtained from simulations, one is able to |
217 |
|
approximate the first and second derivatives of $T$ with finite |
218 |
< |
difference method and thus calculate $G^\prime$. |
218 |
> |
difference methods and thus calculate $G^\prime$. |
219 |
|
|
220 |
< |
In what follows, both definitions are used for calculation and comparison. |
220 |
> |
In what follows, both definitions have been used for calculation and |
221 |
> |
are compared in the results. |
222 |
|
|
223 |
< |
[IMPOSE G DEFINITION INTO OUR SYSTEMS] |
224 |
< |
To facilitate the use of the above definitions in calculating $G$ and |
225 |
< |
$G^\prime$, we have a metal slab with its (111) surfaces perpendicular |
226 |
< |
to the $z$-axis of our simulation cells. With or withour capping |
227 |
< |
agents on the surfaces, the metal slab is solvated with organic |
187 |
< |
solvents, as illustrated in Figure \ref{demoPic}. |
223 |
> |
To compare the above definitions ($G$ and $G^\prime$), we have modeled |
224 |
> |
a metal slab with its (111) surfaces perpendicular to the $z$-axis of |
225 |
> |
our simulation cells. Both with and withour capping agents on the |
226 |
> |
surfaces, the metal slab is solvated with simple organic solvents, as |
227 |
> |
illustrated in Figure \ref{demoPic}. |
228 |
|
|
229 |
|
\begin{figure} |
230 |
|
\includegraphics[width=\linewidth]{demoPic} |
233 |
|
\label{demoPic} |
234 |
|
\end{figure} |
235 |
|
|
236 |
< |
With a simulation cell setup following the above manner, one is able |
237 |
< |
to equilibrate the system and impose an unphysical thermal flux |
238 |
< |
between the liquid and the metal phase with the NIVS algorithm. Under |
239 |
< |
a stablized thermal gradient induced by periodically applying the |
240 |
< |
unphysical flux, one is able to obtain a temperature profile and the |
241 |
< |
physical thermal flux corresponding to it, which equals to the |
242 |
< |
unphysical flux applied by NIVS. These data enables the evaluation of |
243 |
< |
the interfacial thermal conductance of a surface. Figure \ref{gradT} |
204 |
< |
is an example how those stablized thermal gradient can be used to |
205 |
< |
obtain the 1st and 2nd derivatives of the temperature profile. |
236 |
> |
With the simulation cell described above, we are able to equilibrate |
237 |
> |
the system and impose an unphysical thermal flux between the liquid |
238 |
> |
and the metal phase using the NIVS algorithm. By periodically applying |
239 |
> |
the unphysical flux, we are able to obtain a temperature profile and |
240 |
> |
its spatial derivatives. These quantities enable the evaluation of the |
241 |
> |
interfacial thermal conductance of a surface. Figure \ref{gradT} is an |
242 |
> |
example how those applied thermal fluxes can be used to obtain the 1st |
243 |
> |
and 2nd derivatives of the temperature profile. |
244 |
|
|
245 |
|
\begin{figure} |
246 |
|
\includegraphics[width=\linewidth]{gradT} |
250 |
|
\end{figure} |
251 |
|
|
252 |
|
\section{Computational Details} |
253 |
< |
\subsection{System Geometry} |
254 |
< |
In our simulations, Au is used to construct a metal slab with bare |
255 |
< |
(111) surface perpendicular to the $z$-axis. Different slab thickness |
256 |
< |
(layer numbers of Au) are simulated. This metal slab is first |
257 |
< |
equilibrated under normal pressure (1 atm) and a desired |
258 |
< |
temperature. After equilibration, butanethiol is used as the capping |
259 |
< |
agent molecule to cover the bare Au (111) surfaces evenly. The sulfur |
260 |
< |
atoms in the butanethiol molecules would occupy the three-fold sites |
261 |
< |
of the surfaces, and the maximal butanethiol capacity on Au surface is |
262 |
< |
$1/3$ of the total number of surface Au atoms[CITATION]. A series of |
263 |
< |
different coverage surfaces is investigated in order to study the |
264 |
< |
relation between coverage and conductance. |
253 |
> |
\subsection{Simulation Protocol} |
254 |
> |
The NIVS algorithm has been implemented in our MD simulation code, |
255 |
> |
OpenMD\cite{Meineke:2005gd,openmd}, and was used for our |
256 |
> |
simulations. Different slab thickness (layer numbers of Au) were |
257 |
> |
simulated. Metal slabs were first equilibrated under atmospheric |
258 |
> |
pressure (1 atm) and a desired temperature (e.g. 200K). After |
259 |
> |
equilibration, butanethiol capping agents were placed at three-fold |
260 |
> |
sites on the Au(111) surfaces. The maximum butanethiol capacity on Au |
261 |
> |
surface is $1/3$ of the total number of surface Au |
262 |
> |
atoms\cite{vlugt:cpc2007154}. A series of different coverages was |
263 |
> |
investigated in order to study the relation between coverage and |
264 |
> |
interfacial conductance. |
265 |
|
|
266 |
< |
[COVERAGE DISCRIPTION] However, since the interactions between surface |
267 |
< |
Au and butanethiol is non-bonded, the capping agent molecules are |
268 |
< |
allowed to migrate to an empty neighbor three-fold site during a |
269 |
< |
simulation. Therefore, the initial configuration would not severely |
270 |
< |
affect the sampling of a variety of configurations of the same |
271 |
< |
coverage, and the final conductance measurement would be an average |
272 |
< |
effect of these configurations explored in the simulations. [MAY NEED FIGURES] |
266 |
> |
The capping agent molecules were allowed to migrate during the |
267 |
> |
simulations. They distributed themselves uniformly and sampled a |
268 |
> |
number of three-fold sites throughout out study. Therefore, the |
269 |
> |
initial configuration would not noticeably affect the sampling of a |
270 |
> |
variety of configurations of the same coverage, and the final |
271 |
> |
conductance measurement would be an average effect of these |
272 |
> |
configurations explored in the simulations. [MAY NEED FIGURES] |
273 |
|
|
274 |
< |
After the modified Au-butanethiol surface systems are equilibrated |
275 |
< |
under canonical ensemble, Packmol\cite{packmol} is used to pack |
276 |
< |
organic solvent molecules in the previously vacuum part of the |
277 |
< |
simulation cells, which guarantees that short range repulsive |
278 |
< |
interactions do not disrupt the simulations. Two solvents are |
279 |
< |
investigated, one which has little vibrational overlap with the |
242 |
< |
alkanethiol and plane-like shape (toluene), and one which has similar |
243 |
< |
vibrational frequencies and chain-like shape ({\it n}-hexane). The |
244 |
< |
spacing filled by solvent molecules, i.e. the gap between periodically |
245 |
< |
repeated Au-butanethiol surfaces should be carefully chosen so that it |
246 |
< |
would not be too short to affect the liquid phase structure, nor too |
247 |
< |
long, leading to over cooling (freezing) or heating (boiling) when a |
248 |
< |
thermal flux is applied. In our simulations, this spacing is usually |
249 |
< |
$35 \sim 60$\AA. |
274 |
> |
After the modified Au-butanethiol surface systems were equilibrated |
275 |
> |
under canonical ensemble, organic solvent molecules were packed in the |
276 |
> |
previously empty part of the simulation cells\cite{packmol}. Two |
277 |
> |
solvents were investigated, one which has little vibrational overlap |
278 |
> |
with the alkanethiol and a planar shape (toluene), and one which has |
279 |
> |
similar vibrational frequencies and chain-like shape ({\it n}-hexane). |
280 |
|
|
281 |
+ |
The space filled by solvent molecules, i.e. the gap between |
282 |
+ |
periodically repeated Au-butanethiol surfaces should be carefully |
283 |
+ |
chosen. A very long length scale for the thermal gradient axis ($z$) |
284 |
+ |
may cause excessively hot or cold temperatures in the middle of the |
285 |
+ |
solvent region and lead to undesired phenomena such as solvent boiling |
286 |
+ |
or freezing when a thermal flux is applied. Conversely, too few |
287 |
+ |
solvent molecules would change the normal behavior of the liquid |
288 |
+ |
phase. Therefore, our $N_{solvent}$ values were chosen to ensure that |
289 |
+ |
these extreme cases did not happen to our simulations. And the |
290 |
+ |
corresponding spacing is usually $35 \sim 60$\AA. |
291 |
+ |
|
292 |
|
The initial configurations generated by Packmol are further |
293 |
|
equilibrated with the $x$ and $y$ dimensions fixed, only allowing |
294 |
|
length scale change in $z$ dimension. This is to ensure that the |
323 |
|
same type of particles and between particles of different species. |
324 |
|
|
325 |
|
The Au-Au interactions in metal lattice slab is described by the |
326 |
< |
quantum Sutton-Chen (QSC) formulation.\cite{PhysRevB.59.3527} The QSC |
326 |
> |
quantum Sutton-Chen (QSC) formulation\cite{PhysRevB.59.3527}. The QSC |
327 |
|
potentials include zero-point quantum corrections and are |
328 |
|
reparametrized for accurate surface energies compared to the |
329 |
|
Sutton-Chen potentials\cite{Chen90}. |
330 |
|
|
331 |
+ |
Figure \ref{demoMol} demonstrates how we name our pseudo-atoms of the |
332 |
+ |
organic solvent molecules in our simulations. |
333 |
+ |
|
334 |
+ |
\begin{figure} |
335 |
+ |
\includegraphics[width=\linewidth]{demoMol} |
336 |
+ |
\caption{Denomination of atoms or pseudo-atoms in our simulations: a) |
337 |
+ |
UA-hexane; b) AA-hexane; c) UA-toluene; d) AA-toluene.} |
338 |
+ |
\label{demoMol} |
339 |
+ |
\end{figure} |
340 |
+ |
|
341 |
|
For both solvent molecules, straight chain {\it n}-hexane and aromatic |
342 |
|
toluene, United-Atom (UA) and All-Atom (AA) models are used |
343 |
|
respectively. The TraPPE-UA |
351 |
|
to a system, the temperature of ``hot'' area in the liquid phase would be |
352 |
|
significantly higher than the average, to prevent over heating and |
353 |
|
boiling of the liquid phase, the average temperature in our |
354 |
< |
simulations should be much lower than the liquid boiling point. [NEED MORE DISCUSSION] |
354 |
> |
simulations should be much lower than the liquid boiling point. [MORE DISCUSSION] |
355 |
|
For UA-toluene model, rigid body constraints are applied, so that the |
356 |
< |
benzene ring and the methyl-C(aromatic) bond are kept rigid. This |
357 |
< |
would save computational time.[MORE DETAILS NEEDED] |
356 |
> |
benzene ring and the methyl-CRar bond are kept rigid. This would save |
357 |
> |
computational time.[MORE DETAILS] |
358 |
|
|
359 |
|
Besides the TraPPE-UA models, AA models for both organic solvents are |
360 |
< |
included in our studies as well. For hexane, the OPLS |
361 |
< |
all-atom\cite{OPLSAA} force field is used. [MORE DETAILS] |
360 |
> |
included in our studies as well. For hexane, the OPLS-AA\cite{OPLSAA} |
361 |
> |
force field is used. [MORE DETAILS] |
362 |
|
For toluene, the United Force Field developed by Rapp\'{e} {\it et |
363 |
|
al.}\cite{doi:10.1021/ja00051a040} is adopted.[MORE DETAILS] |
364 |
|
|
365 |
|
The capping agent in our simulations, the butanethiol molecules can |
366 |
|
either use UA or AA model. The TraPPE-UA force fields includes |
367 |
< |
parameters for thiol molecules\cite{TraPPE-UA.thiols} and are used in |
368 |
< |
our simulations corresponding to our TraPPE-UA models for solvent. |
369 |
< |
and All-Atom models [NEED CITATIONS] |
370 |
< |
However, the model choice (UA or AA) of capping agent can be different |
371 |
< |
from the solvent. Regardless of model choice, the force field |
372 |
< |
parameters for interactions between capping agent and solvent can be |
373 |
< |
derived using Lorentz-Berthelot Mixing Rule. |
367 |
> |
parameters for thiol molecules\cite{TraPPE-UA.thiols} and are used for |
368 |
> |
UA butanethiol model in our simulations. The OPLS-AA also provides |
369 |
> |
parameters for alkyl thiols. However, alkyl thiols adsorbed on Au(111) |
370 |
> |
surfaces do not have the hydrogen atom bonded to sulfur. To adapt this |
371 |
> |
change and derive suitable parameters for butanethiol adsorbed on |
372 |
> |
Au(111) surfaces, we adopt the S parameters from Luedtke and |
373 |
> |
Landman\cite{landman:1998} and modify parameters for its neighbor C |
374 |
> |
atom for charge balance in the molecule. Note that the model choice |
375 |
> |
(UA or AA) of capping agent can be different from the |
376 |
> |
solvent. Regardless of model choice, the force field parameters for |
377 |
> |
interactions between capping agent and solvent can be derived using |
378 |
> |
Lorentz-Berthelot Mixing Rule:[EQN'S] |
379 |
|
|
380 |
+ |
|
381 |
|
To describe the interactions between metal Au and non-metal capping |
382 |
< |
agent and solvent, we refer to Vlugt\cite{vlugt:cpc2007154} and derive |
383 |
< |
other interactions which are not yet finely parametrized. [can add |
384 |
< |
hautman and klein's paper here and more discussion; need to put |
385 |
< |
aromatic-metal interaction approximation here]\cite{doi:10.1021/jp034405s} |
382 |
> |
agent and solvent particles, we refer to an adsorption study of alkyl |
383 |
> |
thiols on gold surfaces by Vlugt {\it et |
384 |
> |
al.}\cite{vlugt:cpc2007154} They fitted an effective Lennard-Jones |
385 |
> |
form of potential parameters for the interaction between Au and |
386 |
> |
pseudo-atoms CH$_x$ and S based on a well-established and widely-used |
387 |
> |
effective potential of Hautman and Klein\cite{hautman:4994} for the |
388 |
> |
Au(111) surface. As our simulations require the gold lattice slab to |
389 |
> |
be non-rigid so that it could accommodate kinetic energy for thermal |
390 |
> |
transport study purpose, the pair-wise form of potentials is |
391 |
> |
preferred. |
392 |
|
|
393 |
< |
[TABULATED FORCE FIELD PARAMETERS NEEDED] |
393 |
> |
Besides, the potentials developed from {\it ab initio} calculations by |
394 |
> |
Leng {\it et al.}\cite{doi:10.1021/jp034405s} are adopted for the |
395 |
> |
interactions between Au and aromatic C/H atoms in toluene.[MORE DETAILS] |
396 |
|
|
397 |
+ |
However, the Lennard-Jones parameters between Au and other types of |
398 |
+ |
particles in our simulations are not yet well-established. For these |
399 |
+ |
interactions, we attempt to derive their parameters using the Mixing |
400 |
+ |
Rule. To do this, the ``Metal-non-Metal'' (MnM) interaction parameters |
401 |
+ |
for Au is first extracted from the Au-CH$_x$ parameters by applying |
402 |
+ |
the Mixing Rule reversely. Table \ref{MnM} summarizes these ``MnM'' |
403 |
+ |
parameters in our simulations. |
404 |
|
|
405 |
< |
[SURFACE RECONSTRUCTION PREVENTS SIMULATION TEMP TO GO HIGHER] |
405 |
> |
\begin{table*} |
406 |
> |
\begin{minipage}{\linewidth} |
407 |
> |
\begin{center} |
408 |
> |
\caption{Lennard-Jones parameters for Au-non-Metal |
409 |
> |
interactions in our simulations.} |
410 |
> |
|
411 |
> |
\begin{tabular}{ccc} |
412 |
> |
\hline\hline |
413 |
> |
Non-metal atom & $\sigma$ & $\epsilon$ \\ |
414 |
> |
(or pseudo-atom) & \AA & kcal/mol \\ |
415 |
> |
\hline |
416 |
> |
S & 2.40 & 8.465 \\ |
417 |
> |
CH3 & 3.54 & 0.2146 \\ |
418 |
> |
CH2 & 3.54 & 0.1749 \\ |
419 |
> |
CT3 & 3.365 & 0.1373 \\ |
420 |
> |
CT2 & 3.365 & 0.1373 \\ |
421 |
> |
CTT & 3.365 & 0.1373 \\ |
422 |
> |
HC & 2.865 & 0.09256 \\ |
423 |
> |
CHar & 3.4625 & 0.1680 \\ |
424 |
> |
CRar & 3.555 & 0.1604 \\ |
425 |
> |
CA & 3.173 & 0.0640 \\ |
426 |
> |
HA & 2.746 & 0.0414 \\ |
427 |
> |
\hline\hline |
428 |
> |
\end{tabular} |
429 |
> |
\label{MnM} |
430 |
> |
\end{center} |
431 |
> |
\end{minipage} |
432 |
> |
\end{table*} |
433 |
|
|
434 |
|
|
435 |
< |
\section{Results} |
436 |
< |
[REARRANGEMENT NEEDED] |
437 |
< |
\subsection{Toluene Solvent} |
435 |
> |
\section{Results and Discussions} |
436 |
> |
[MAY HAVE A BRIEF SUMMARY] |
437 |
> |
\subsection{How Simulation Parameters Affects $G$} |
438 |
> |
[MAY NOT PUT AT FIRST] |
439 |
> |
We have varied our protocol or other parameters of the simulations in |
440 |
> |
order to investigate how these factors would affect the measurement of |
441 |
> |
$G$'s. It turned out that while some of these parameters would not |
442 |
> |
affect the results substantially, some other changes to the |
443 |
> |
simulations would have a significant impact on the measurement |
444 |
> |
results. |
445 |
|
|
446 |
< |
The results (Table \ref{AuThiolToluene}) show a |
447 |
< |
significant conductance enhancement compared to the gold/water |
448 |
< |
interface without capping agent and agree with available experimental |
449 |
< |
data. This indicates that the metal-metal potential, though not |
450 |
< |
predicting an accurate bulk metal thermal conductivity, does not |
451 |
< |
greatly interfere with the simulation of the thermal conductance |
452 |
< |
behavior across a non-metal interface. The solvent model is not |
453 |
< |
particularly volatile, so the simulation cell does not expand |
454 |
< |
significantly under higher temperature. We did not observe a |
349 |
< |
significant conductance decrease when the temperature was increased to |
350 |
< |
300K. The results show that the two definitions used for $G$ yield |
351 |
< |
comparable values, though $G^\prime$ tends to be smaller. |
446 |
> |
In some of our simulations, we allowed $L_x$ and $L_y$ to change |
447 |
> |
during equilibrating the liquid phase. Due to the stiffness of the Au |
448 |
> |
slab, $L_x$ and $L_y$ would not change noticeably after |
449 |
> |
equilibration. Although $L_z$ could fluctuate $\sim$1\% after a system |
450 |
> |
is fully equilibrated in the NPT ensemble, this fluctuation, as well |
451 |
> |
as those comparably smaller to $L_x$ and $L_y$, would not be magnified |
452 |
> |
on the calculated $G$'s, as shown in Table \ref{AuThiolHexaneUA}. This |
453 |
> |
insensivity to $L_i$ fluctuations allows reliable measurement of $G$'s |
454 |
> |
without the necessity of extremely cautious equilibration process. |
455 |
|
|
456 |
+ |
As stated in our computational details, the spacing filled with |
457 |
+ |
solvent molecules can be chosen within a range. This allows some |
458 |
+ |
change of solvent molecule numbers for the same Au-butanethiol |
459 |
+ |
surfaces. We did this study on our Au-butanethiol/hexane |
460 |
+ |
simulations. Nevertheless, the results obtained from systems of |
461 |
+ |
different $N_{hexane}$ did not indicate that the measurement of $G$ is |
462 |
+ |
susceptible to this parameter. For computational efficiency concern, |
463 |
+ |
smaller system size would be preferable, given that the liquid phase |
464 |
+ |
structure is not affected. |
465 |
+ |
|
466 |
+ |
Our NIVS algorithm allows change of unphysical thermal flux both in |
467 |
+ |
direction and in quantity. This feature extends our investigation of |
468 |
+ |
interfacial thermal conductance. However, the magnitude of this |
469 |
+ |
thermal flux is not arbitary if one aims to obtain a stable and |
470 |
+ |
reliable thermal gradient. A temperature profile would be |
471 |
+ |
substantially affected by noise when $|J_z|$ has a much too low |
472 |
+ |
magnitude; while an excessively large $|J_z|$ that overwhelms the |
473 |
+ |
conductance capacity of the interface would prevent a thermal gradient |
474 |
+ |
to reach a stablized steady state. NIVS has the advantage of allowing |
475 |
+ |
$J$ to vary in a wide range such that the optimal flux range for $G$ |
476 |
+ |
measurement can generally be simulated by the algorithm. Within the |
477 |
+ |
optimal range, we were able to study how $G$ would change according to |
478 |
+ |
the thermal flux across the interface. For our simulations, we denote |
479 |
+ |
$J_z$ to be positive when the physical thermal flux is from the liquid |
480 |
+ |
to metal, and negative vice versa. The $G$'s measured under different |
481 |
+ |
$J_z$ is listed in Table \ref{AuThiolHexaneUA} and [REF]. These |
482 |
+ |
results do not suggest that $G$ is dependent on $J_z$ within this flux |
483 |
+ |
range. The linear response of flux to thermal gradient simplifies our |
484 |
+ |
investigations in that we can rely on $G$ measurement with only a |
485 |
+ |
couple $J_z$'s and do not need to test a large series of fluxes. |
486 |
+ |
|
487 |
+ |
%ADD MORE TO TABLE |
488 |
|
\begin{table*} |
489 |
|
\begin{minipage}{\linewidth} |
490 |
|
\begin{center} |
491 |
|
\caption{Computed interfacial thermal conductivity ($G$ and |
492 |
< |
$G^\prime$) values for the Au/butanethiol/toluene interface at |
493 |
< |
different temperatures using a range of energy fluxes.} |
492 |
> |
$G^\prime$) values for the 100\% covered Au-butanethiol/hexane |
493 |
> |
interfaces with UA model and different hexane molecule numbers |
494 |
> |
at different temperatures using a range of energy fluxes.} |
495 |
|
|
496 |
+ |
\begin{tabular}{cccccccc} |
497 |
+ |
\hline\hline |
498 |
+ |
$\langle T\rangle$ & & $L_x$ & $L_y$ & $L_z$ & $J_z$ & |
499 |
+ |
$G$ & $G^\prime$ \\ |
500 |
+ |
(K) & $N_{hexane}$ & \multicolumn{3}{c}{(\AA)} & (GW/m$^2$) & |
501 |
+ |
\multicolumn{2}{c}{(MW/m$^2$/K)} \\ |
502 |
+ |
\hline |
503 |
+ |
200 & 266 & 29.86 & 25.80 & 113.1 & -0.96 & |
504 |
+ |
102() & 80.0() \\ |
505 |
+ |
& 200 & 29.84 & 25.81 & 93.9 & 1.92 & |
506 |
+ |
129() & 87.3() \\ |
507 |
+ |
& & 29.84 & 25.81 & 95.3 & 1.93 & |
508 |
+ |
131() & 77.5() \\ |
509 |
+ |
& 166 & 29.84 & 25.81 & 85.7 & 0.97 & |
510 |
+ |
115() & 69.3() \\ |
511 |
+ |
& & & & & 1.94 & |
512 |
+ |
125() & 87.1() \\ |
513 |
+ |
250 & 200 & 29.84 & 25.87 & 106.8 & 0.96 & |
514 |
+ |
81.8() & 67.0() \\ |
515 |
+ |
& 166 & 29.87 & 25.84 & 94.8 & 0.98 & |
516 |
+ |
79.0() & 62.9() \\ |
517 |
+ |
& & 29.84 & 25.85 & 95.0 & 1.44 & |
518 |
+ |
76.2() & 64.8() \\ |
519 |
+ |
\hline\hline |
520 |
+ |
\end{tabular} |
521 |
+ |
\label{AuThiolHexaneUA} |
522 |
+ |
\end{center} |
523 |
+ |
\end{minipage} |
524 |
+ |
\end{table*} |
525 |
+ |
|
526 |
+ |
Furthermore, we also attempted to increase system average temperatures |
527 |
+ |
to above 200K. These simulations are first equilibrated in the NPT |
528 |
+ |
ensemble under normal pressure. As stated above, the TraPPE-UA model |
529 |
+ |
for hexane tends to predict a lower boiling point. In our simulations, |
530 |
+ |
hexane had diffculty to remain in liquid phase when NPT equilibration |
531 |
+ |
temperature is higher than 250K. Additionally, the equilibrated liquid |
532 |
+ |
hexane density under 250K becomes lower than experimental value. This |
533 |
+ |
expanded liquid phase leads to lower contact between hexane and |
534 |
+ |
butanethiol as well.[MAY NEED FIGURE] And this reduced contact would |
535 |
+ |
probably be accountable for a lower interfacial thermal conductance, |
536 |
+ |
as shown in Table \ref{AuThiolHexaneUA}. |
537 |
+ |
|
538 |
+ |
A similar study for TraPPE-UA toluene agrees with the above result as |
539 |
+ |
well. Having a higher boiling point, toluene tends to remain liquid in |
540 |
+ |
our simulations even equilibrated under 300K in NPT |
541 |
+ |
ensembles. Furthermore, the expansion of the toluene liquid phase is |
542 |
+ |
not as significant as that of the hexane. This prevents severe |
543 |
+ |
decrease of liquid-capping agent contact and the results (Table |
544 |
+ |
\ref{AuThiolToluene}) show only a slightly decreased interface |
545 |
+ |
conductance. Therefore, solvent-capping agent contact should play an |
546 |
+ |
important role in the thermal transport process across the interface |
547 |
+ |
in that higher degree of contact could yield increased conductance. |
548 |
+ |
|
549 |
+ |
[ADD Lxyz AND ERROR ESTIMATE TO TABLE] |
550 |
+ |
\begin{table*} |
551 |
+ |
\begin{minipage}{\linewidth} |
552 |
+ |
\begin{center} |
553 |
+ |
\caption{Computed interfacial thermal conductivity ($G$ and |
554 |
+ |
$G^\prime$) values for a 90\% coverage Au-butanethiol/toluene |
555 |
+ |
interface at different temperatures using a range of energy |
556 |
+ |
fluxes.} |
557 |
+ |
|
558 |
|
\begin{tabular}{cccc} |
559 |
|
\hline\hline |
560 |
|
$\langle T\rangle$ & $J_z$ & $G$ & $G^\prime$ \\ |
561 |
|
(K) & (GW/m$^2$) & \multicolumn{2}{c}{(MW/m$^2$/K)} \\ |
562 |
|
\hline |
563 |
< |
200 & 1.86 & 180 & 135 \\ |
564 |
< |
& 2.15 & 204 & 113 \\ |
565 |
< |
& 3.93 & 175 & 114 \\ |
566 |
< |
300 & 1.91 & 143 & 125 \\ |
567 |
< |
& 4.19 & 134 & 113 \\ |
563 |
> |
200 & -1.86 & 180() & 135() \\ |
564 |
> |
& 2.15 & 204() & 113() \\ |
565 |
> |
& -3.93 & 175() & 114() \\ |
566 |
> |
300 & -1.91 & 143() & 125() \\ |
567 |
> |
& -4.19 & 134() & 113() \\ |
568 |
|
\hline\hline |
569 |
|
\end{tabular} |
570 |
|
\label{AuThiolToluene} |
572 |
|
\end{minipage} |
573 |
|
\end{table*} |
574 |
|
|
575 |
< |
\subsection{Hexane Solvent} |
575 |
> |
Besides lower interfacial thermal conductance, surfaces in relatively |
576 |
> |
high temperatures are susceptible to reconstructions, when |
577 |
> |
butanethiols have a full coverage on the Au(111) surface. These |
578 |
> |
reconstructions include surface Au atoms migrated outward to the S |
579 |
> |
atom layer, and butanethiol molecules embedded into the original |
580 |
> |
surface Au layer. The driving force for this behavior is the strong |
581 |
> |
Au-S interactions in our simulations. And these reconstructions lead |
582 |
> |
to higher ratio of Au-S attraction and thus is energetically |
583 |
> |
favorable. Furthermore, this phenomenon agrees with experimental |
584 |
> |
results\cite{doi:10.1021/j100035a033,doi:10.1021/la026493y}. Vlugt |
585 |
> |
{\it et al.} had kept their Au(111) slab rigid so that their |
586 |
> |
simulations can reach 300K without surface reconstructions. Without |
587 |
> |
this practice, simulating 100\% thiol covered interfaces under higher |
588 |
> |
temperatures could hardly avoid surface reconstructions. However, our |
589 |
> |
measurement is based on assuming homogeneity on $x$ and $y$ dimensions |
590 |
> |
so that measurement of $T$ at particular $z$ would be an effective |
591 |
> |
average of the particles of the same type. Since surface |
592 |
> |
reconstructions could eliminate the original $x$ and $y$ dimensional |
593 |
> |
homogeneity, measurement of $G$ is more difficult to conduct under |
594 |
> |
higher temperatures. Therefore, most of our measurements are |
595 |
> |
undertaken at $\langle T\rangle\sim$200K. |
596 |
|
|
597 |
< |
Using the united-atom model, different coverages of capping agent, |
598 |
< |
temperatures of simulations and numbers of solvent molecules were all |
599 |
< |
investigated and Table \ref{AuThiolHexaneUA} shows the results of |
600 |
< |
these computations. The number of hexane molecules in our simulations |
601 |
< |
does not affect the calculations significantly. However, a very long |
602 |
< |
length scale for the thermal gradient axis ($z$) may cause excessively |
603 |
< |
hot or cold temperatures in the middle of the solvent region and lead |
604 |
< |
to undesired phenomena such as solvent boiling or freezing, while too |
605 |
< |
few solvent molecules would change the normal behavior of the liquid |
606 |
< |
phase. Our $N_{hexane}$ values were chosen to ensure that these |
389 |
< |
extreme cases did not happen to our simulations. |
597 |
> |
However, when the surface is not completely covered by butanethiols, |
598 |
> |
the simulated system is more resistent to the reconstruction |
599 |
> |
above. Our Au-butanethiol/toluene system did not see this phenomena |
600 |
> |
even at $\langle T\rangle\sim$300K. The Au(111) surfaces have a 90\% coverage of |
601 |
> |
butanethiols and have empty three-fold sites. These empty sites could |
602 |
> |
help prevent surface reconstruction in that they provide other means |
603 |
> |
of capping agent relaxation. It is observed that butanethiols can |
604 |
> |
migrate to their neighbor empty sites during a simulation. Therefore, |
605 |
> |
we were able to obtain $G$'s for these interfaces even at a relatively |
606 |
> |
high temperature without being affected by surface reconstructions. |
607 |
|
|
608 |
< |
Table \ref{AuThiolHexaneUA} enables direct comparison between |
609 |
< |
different coverages of capping agent, when other system parameters are |
610 |
< |
held constant. With high coverage of butanethiol on the gold surface, |
611 |
< |
the interfacial thermal conductance is enhanced |
612 |
< |
significantly. Interestingly, a slightly lower butanethiol coverage |
613 |
< |
leads to a moderately higher conductivity. This is probably due to |
614 |
< |
more solvent/capping agent contact when butanethiol molecules are |
615 |
< |
not densely packed, which enhances the interactions between the two |
616 |
< |
phases and lowers the thermal transfer barrier of this interface. |
617 |
< |
% [COMPARE TO AU/WATER IN PAPER] |
608 |
> |
\subsection{Influence of Capping Agent Coverage on $G$} |
609 |
> |
To investigate the influence of butanethiol coverage on interfacial |
610 |
> |
thermal conductance, a series of different coverage Au-butanethiol |
611 |
> |
surfaces is prepared and solvated with various organic |
612 |
> |
molecules. These systems are then equilibrated and their interfacial |
613 |
> |
thermal conductivity are measured with our NIVS algorithm. Table |
614 |
> |
\ref{tlnUhxnUhxnD} lists these results for direct comparison between |
615 |
> |
different coverages of butanethiol. To study the isotope effect in |
616 |
> |
interfacial thermal conductance, deuterated UA-hexane is included as |
617 |
> |
well. |
618 |
|
|
619 |
< |
It is also noted that the overall simulation temperature is another |
620 |
< |
factor that affects the interfacial thermal conductance. One |
621 |
< |
possibility of this effect may be rooted in the decrease in density of |
622 |
< |
the liquid phase. We observed that when the average temperature |
623 |
< |
increases from 200K to 250K, the bulk hexane density becomes lower |
624 |
< |
than experimental value, as the system is equilibrated under NPT |
625 |
< |
ensemble. This leads to lower contact between solvent and capping |
409 |
< |
agent, and thus lower conductivity. |
619 |
> |
It turned out that with partial covered butanethiol on the Au(111) |
620 |
> |
surface, the derivative definition for $G$ (Eq. \ref{derivativeG}) has |
621 |
> |
difficulty to apply, due to the difficulty in locating the maximum of |
622 |
> |
change of $\lambda$. Instead, the discrete definition |
623 |
> |
(Eq. \ref{discreteG}) is easier to apply, as max($\Delta T$) can still |
624 |
> |
be well-defined. Therefore, $G$'s (not $G^\prime$) are used for this |
625 |
> |
section. |
626 |
|
|
627 |
< |
Conductivity values are more difficult to obtain under higher |
628 |
< |
temperatures. This is because the Au surface tends to undergo |
629 |
< |
reconstructions in relatively high temperatures. Surface Au atoms can |
630 |
< |
migrate outward to reach higher Au-S contact; and capping agent |
631 |
< |
molecules can be embedded into the surface Au layer due to the same |
632 |
< |
driving force. This phenomenon agrees with experimental |
417 |
< |
results\cite{doi:10.1021/j100035a033,doi:10.1021/la026493y}. A surface |
418 |
< |
fully covered in capping agent is more susceptible to reconstruction, |
419 |
< |
possibly because fully coverage prevents other means of capping agent |
420 |
< |
relaxation, such as migration to an empty neighbor three-fold site. |
627 |
> |
From Table \ref{tlnUhxnUhxnD}, one can see the significance of the |
628 |
> |
presence of capping agents. Even when a fraction of the Au(111) |
629 |
> |
surface sites are covered with butanethiols, the conductivity would |
630 |
> |
see an enhancement by at least a factor of 3. This indicates the |
631 |
> |
important role cappping agent is playing for thermal transport |
632 |
> |
phenomena on metal/organic solvent surfaces. |
633 |
|
|
634 |
< |
%MAY ADD MORE DATA TO TABLE |
634 |
> |
Interestingly, as one could observe from our results, the maximum |
635 |
> |
conductance enhancement (largest $G$) happens while the surfaces are |
636 |
> |
about 75\% covered with butanethiols. This again indicates that |
637 |
> |
solvent-capping agent contact has an important role of the thermal |
638 |
> |
transport process. Slightly lower butanethiol coverage allows small |
639 |
> |
gaps between butanethiols to form. And these gaps could be filled with |
640 |
> |
solvent molecules, which acts like ``heat conductors'' on the |
641 |
> |
surface. The higher degree of interaction between these solvent |
642 |
> |
molecules and capping agents increases the enhancement effect and thus |
643 |
> |
produces a higher $G$ than densely packed butanethiol arrays. However, |
644 |
> |
once this maximum conductance enhancement is reached, $G$ decreases |
645 |
> |
when butanethiol coverage continues to decrease. Each capping agent |
646 |
> |
molecule reaches its maximum capacity for thermal |
647 |
> |
conductance. Therefore, even higher solvent-capping agent contact |
648 |
> |
would not offset this effect. Eventually, when butanethiol coverage |
649 |
> |
continues to decrease, solvent-capping agent contact actually |
650 |
> |
decreases with the disappearing of butanethiol molecules. In this |
651 |
> |
case, $G$ decrease could not be offset but instead accelerated. |
652 |
> |
|
653 |
> |
A comparison of the results obtained from differenet organic solvents |
654 |
> |
can also provide useful information of the interfacial thermal |
655 |
> |
transport process. The deuterated hexane (UA) results do not appear to |
656 |
> |
be much different from those of normal hexane (UA), given that |
657 |
> |
butanethiol (UA) is non-deuterated for both solvents. These UA model |
658 |
> |
studies, even though eliminating C-H vibration samplings, still have |
659 |
> |
C-C vibrational frequencies different from each other. However, these |
660 |
> |
differences in the infrared range do not seem to produce an observable |
661 |
> |
difference for the results of $G$. [MAY NEED FIGURE] |
662 |
> |
|
663 |
> |
Furthermore, results for rigid body toluene solvent, as well as other |
664 |
> |
UA-hexane solvents, are reasonable within the general experimental |
665 |
> |
ranges[CITATIONS]. This suggests that explicit hydrogen might not be a |
666 |
> |
required factor for modeling thermal transport phenomena of systems |
667 |
> |
such as Au-thiol/organic solvent. |
668 |
> |
|
669 |
> |
However, results for Au-butanethiol/toluene do not show an identical |
670 |
> |
trend with those for Au-butanethiol/hexane in that $G$'s remain at |
671 |
> |
approximately the same magnitue when butanethiol coverage differs from |
672 |
> |
25\% to 75\%. This might be rooted in the molecule shape difference |
673 |
> |
for plane-like toluene and chain-like {\it n}-hexane. Due to this |
674 |
> |
difference, toluene molecules have more difficulty in occupying |
675 |
> |
relatively small gaps among capping agents when their coverage is not |
676 |
> |
too low. Therefore, the solvent-capping agent contact may keep |
677 |
> |
increasing until the capping agent coverage reaches a relatively low |
678 |
> |
level. This becomes an offset for decreasing butanethiol molecules on |
679 |
> |
its effect to the process of interfacial thermal transport. Thus, one |
680 |
> |
can see a plateau of $G$ vs. butanethiol coverage in our results. |
681 |
> |
|
682 |
> |
[NEED ERROR ESTIMATE, MAY ALSO PUT J HERE] |
683 |
|
\begin{table*} |
684 |
|
\begin{minipage}{\linewidth} |
685 |
|
\begin{center} |
686 |
< |
\caption{Computed interfacial thermal conductivity ($G$ and |
687 |
< |
$G^\prime$) values for the Au/butanethiol/hexane interface |
688 |
< |
with united-atom model and different capping agent coverage |
689 |
< |
and solvent molecule numbers at different temperatures using a |
430 |
< |
range of energy fluxes.} |
686 |
> |
\caption{Computed interfacial thermal conductivity ($G$) values |
687 |
> |
for the Au-butanethiol/solvent interface with various UA |
688 |
> |
models and different capping agent coverages at $\langle |
689 |
> |
T\rangle\sim$200K using certain energy flux respectively.} |
690 |
|
|
691 |
< |
\begin{tabular}{cccccc} |
691 |
> |
\begin{tabular}{cccc} |
692 |
|
\hline\hline |
693 |
< |
Thiol & $\langle T\rangle$ & & $J_z$ & $G$ & $G^\prime$ \\ |
694 |
< |
coverage (\%) & (K) & $N_{hexane}$ & (GW/m$^2$) & |
436 |
< |
\multicolumn{2}{c}{(MW/m$^2$/K)} \\ |
693 |
> |
Thiol & \multicolumn{3}{c}{$G$(MW/m$^2$/K)} \\ |
694 |
> |
coverage (\%) & hexane & hexane(D) & toluene \\ |
695 |
|
\hline |
696 |
< |
0.0 & 200 & 200 & 0.96 & 43.3 & 42.7 \\ |
697 |
< |
& & & 1.91 & 45.7 & 42.9 \\ |
698 |
< |
& & 166 & 0.96 & 43.1 & 53.4 \\ |
699 |
< |
88.9 & 200 & 166 & 1.94 & 172 & 108 \\ |
700 |
< |
100.0 & 250 & 200 & 0.96 & 81.8 & 67.0 \\ |
701 |
< |
& & 166 & 0.98 & 79.0 & 62.9 \\ |
444 |
< |
& & & 1.44 & 76.2 & 64.8 \\ |
445 |
< |
& 200 & 200 & 1.92 & 129 & 87.3 \\ |
446 |
< |
& & & 1.93 & 131 & 77.5 \\ |
447 |
< |
& & 166 & 0.97 & 115 & 69.3 \\ |
448 |
< |
& & & 1.94 & 125 & 87.1 \\ |
696 |
> |
0.0 & 46.5() & 43.9() & 70.1() \\ |
697 |
> |
25.0 & 151() & 153() & 249() \\ |
698 |
> |
50.0 & 172() & 182() & 214() \\ |
699 |
> |
75.0 & 242() & 229() & 244() \\ |
700 |
> |
88.9 & 178() & - & - \\ |
701 |
> |
100.0 & 137() & 153() & 187() \\ |
702 |
|
\hline\hline |
703 |
|
\end{tabular} |
704 |
< |
\label{AuThiolHexaneUA} |
704 |
> |
\label{tlnUhxnUhxnD} |
705 |
|
\end{center} |
706 |
|
\end{minipage} |
707 |
|
\end{table*} |
708 |
|
|
709 |
< |
For the all-atom model, the liquid hexane phase was not stable under NPT |
710 |
< |
conditions. Therefore, the simulation length scale parameters are |
458 |
< |
adopted from previous equilibration results of the united-atom model |
459 |
< |
at 200K. Table \ref{AuThiolHexaneAA} shows the results of these |
460 |
< |
simulations. The conductivity values calculated with full capping |
461 |
< |
agent coverage are substantially larger than observed in the |
462 |
< |
united-atom model, and is even higher than predicted by |
463 |
< |
experiments. It is possible that our parameters for metal-non-metal |
464 |
< |
particle interactions lead to an overestimate of the interfacial |
465 |
< |
thermal conductivity, although the active C-H vibrations in the |
466 |
< |
all-atom model (which should not be appreciably populated at normal |
467 |
< |
temperatures) could also account for this high conductivity. The major |
468 |
< |
thermal transfer barrier of Au/butanethiol/hexane interface is between |
469 |
< |
the liquid phase and the capping agent, so extra degrees of freedom |
470 |
< |
such as the C-H vibrations could enhance heat exchange between these |
471 |
< |
two phases and result in a much higher conductivity. |
709 |
> |
\subsection{Influence of Chosen Molecule Model on $G$} |
710 |
> |
[MAY COMBINE W MECHANISM STUDY] |
711 |
|
|
712 |
+ |
In addition to UA solvent/capping agent models, AA models are included |
713 |
+ |
in our simulations as well. Besides simulations of the same (UA or AA) |
714 |
+ |
model for solvent and capping agent, different models can be applied |
715 |
+ |
to different components. Furthermore, regardless of models chosen, |
716 |
+ |
either the solvent or the capping agent can be deuterated, similar to |
717 |
+ |
the previous section. Table \ref{modelTest} summarizes the results of |
718 |
+ |
these studies. |
719 |
+ |
|
720 |
+ |
[MORE DATA; ERROR ESTIMATE] |
721 |
|
\begin{table*} |
722 |
|
\begin{minipage}{\linewidth} |
723 |
|
\begin{center} |
724 |
|
|
725 |
|
\caption{Computed interfacial thermal conductivity ($G$ and |
726 |
< |
$G^\prime$) values for the Au/butanethiol/hexane interface |
727 |
< |
with all-atom model and different capping agent coverage at |
728 |
< |
200K using a range of energy fluxes.} |
726 |
> |
$G^\prime$) values for interfaces using various models for |
727 |
> |
solvent and capping agent (or without capping agent) at |
728 |
> |
$\langle T\rangle\sim$200K.} |
729 |
|
|
730 |
< |
\begin{tabular}{cccc} |
730 |
> |
\begin{tabular}{ccccc} |
731 |
|
\hline\hline |
732 |
< |
Thiol & $J_z$ & $G$ & $G^\prime$ \\ |
733 |
< |
coverage (\%) & (GW/m$^2$) & \multicolumn{2}{c}{(MW/m$^2$/K)} \\ |
732 |
> |
Butanethiol model & Solvent & $J_z$ & $G$ & $G^\prime$ \\ |
733 |
> |
(or bare surface) & model & (GW/m$^2$) & |
734 |
> |
\multicolumn{2}{c}{(MW/m$^2$/K)} \\ |
735 |
|
\hline |
736 |
< |
0.0 & 0.95 & 28.5 & 27.2 \\ |
737 |
< |
& 1.88 & 30.3 & 28.9 \\ |
738 |
< |
100.0 & 2.87 & 551 & 294 \\ |
739 |
< |
& 3.81 & 494 & 193 \\ |
736 |
> |
UA & AA hexane & 1.94 & 135() & 129() \\ |
737 |
> |
& & 2.86 & 126() & 115() \\ |
738 |
> |
& AA toluene & 1.89 & 200() & 149() \\ |
739 |
> |
AA & UA hexane & 1.94 & 116() & 129() \\ |
740 |
> |
& AA hexane & 3.76 & 451() & 378() \\ |
741 |
> |
& & 4.71 & 432() & 334() \\ |
742 |
> |
& AA toluene & 3.79 & 487() & 290() \\ |
743 |
> |
AA(D) & UA hexane & 1.94 & 158() & 172() \\ |
744 |
> |
bare & AA hexane & 0.96 & 31.0() & 29.4() \\ |
745 |
|
\hline\hline |
746 |
|
\end{tabular} |
747 |
< |
\label{AuThiolHexaneAA} |
747 |
> |
\label{modelTest} |
748 |
|
\end{center} |
749 |
|
\end{minipage} |
750 |
|
\end{table*} |
751 |
|
|
752 |
< |
%subsubsection{Vibrational spectrum study on conductance mechanism} |
752 |
> |
To facilitate direct comparison, the same system with differnt models |
753 |
> |
for different components uses the same length scale for their |
754 |
> |
simulation cells. Without the presence of capping agent, using |
755 |
> |
different models for hexane yields similar results for both $G$ and |
756 |
> |
$G^\prime$, and these two definitions agree with eath other very |
757 |
> |
well. This indicates very weak interaction between the metal and the |
758 |
> |
solvent, and is a typical case for acoustic impedance mismatch between |
759 |
> |
these two phases. |
760 |
> |
|
761 |
> |
As for Au(111) surfaces completely covered by butanethiols, the choice |
762 |
> |
of models for capping agent and solvent could impact the measurement |
763 |
> |
of $G$ and $G^\prime$ quite significantly. For Au-butanethiol/hexane |
764 |
> |
interfaces, using AA model for both butanethiol and hexane yields |
765 |
> |
substantially higher conductivity values than using UA model for at |
766 |
> |
least one component of the solvent and capping agent, which exceeds |
767 |
> |
the upper bond of experimental value range. This is probably due to |
768 |
> |
the classically treated C-H vibrations in the AA model, which should |
769 |
> |
not be appreciably populated at normal temperatures. In comparison, |
770 |
> |
once either the hexanes or the butanethiols are deuterated, one can |
771 |
> |
see a significantly lower $G$ and $G^\prime$. In either of these |
772 |
> |
cases, the C-H(D) vibrational overlap between the solvent and the |
773 |
> |
capping agent is removed. [MAY NEED FIGURE] Conclusively, the |
774 |
> |
improperly treated C-H vibration in the AA model produced |
775 |
> |
over-predicted results accordingly. Compared to the AA model, the UA |
776 |
> |
model yields more reasonable results with higher computational |
777 |
> |
efficiency. |
778 |
> |
|
779 |
> |
However, for Au-butanethiol/toluene interfaces, having the AA |
780 |
> |
butanethiol deuterated did not yield a significant change in the |
781 |
> |
measurement results. |
782 |
> |
. , so extra degrees of freedom |
783 |
> |
such as the C-H vibrations could enhance heat exchange between these |
784 |
> |
two phases and result in a much higher conductivity. |
785 |
> |
|
786 |
> |
|
787 |
> |
Although the QSC model for Au is known to predict an overly low value |
788 |
> |
for bulk metal gold conductivity[CITE NIVSRNEMD], our computational |
789 |
> |
results for $G$ and $G^\prime$ do not seem to be affected by this |
790 |
> |
drawback of the model for metal. Instead, the modeling of interfacial |
791 |
> |
thermal transport behavior relies mainly on an accurate description of |
792 |
> |
the interactions between components occupying the interfaces. |
793 |
> |
|
794 |
> |
\subsection{Mechanism of Interfacial Thermal Conductance Enhancement |
795 |
> |
by Capping Agent} |
796 |
> |
%OR\subsection{Vibrational spectrum study on conductance mechanism} |
797 |
> |
|
798 |
> |
[MAY INTRODUCE PROTOCOL IN METHODOLOGY/COMPUTATIONAL DETAIL, EQN'S] |
799 |
> |
|
800 |
|
To investigate the mechanism of this interfacial thermal conductance, |
801 |
|
the vibrational spectra of various gold systems were obtained and are |
802 |
|
shown as in the upper panel of Fig. \ref{vibration}. To obtain these |
803 |
|
spectra, one first runs a simulation in the NVE ensemble and collects |
804 |
|
snapshots of configurations; these configurations are used to compute |
805 |
|
the velocity auto-correlation functions, which is used to construct a |
806 |
< |
power spectrum via a Fourier transform. The gold surfaces covered by |
506 |
< |
butanethiol molecules exhibit an additional peak observed at a |
507 |
< |
frequency of $\sim$170cm$^{-1}$, which is attributed to the vibration |
508 |
< |
of the S-Au bond. This vibration enables efficient thermal transport |
509 |
< |
from surface Au atoms to the capping agents. Simultaneously, as shown |
510 |
< |
in the lower panel of Fig. \ref{vibration}, the large overlap of the |
511 |
< |
vibration spectra of butanethiol and hexane in the all-atom model, |
512 |
< |
including the C-H vibration, also suggests high thermal exchange |
513 |
< |
efficiency. The combination of these two effects produces the drastic |
514 |
< |
interfacial thermal conductance enhancement in the all-atom model. |
806 |
> |
power spectrum via a Fourier transform. |
807 |
|
|
808 |
+ |
The gold surfaces covered by |
809 |
+ |
butanethiol molecules, compared to bare gold surfaces, exhibit an |
810 |
+ |
additional peak observed at a frequency of $\sim$170cm$^{-1}$, which |
811 |
+ |
is attributed to the vibration of the S-Au bond. This vibration |
812 |
+ |
enables efficient thermal transport from surface Au atoms to the |
813 |
+ |
capping agents. Simultaneously, as shown in the lower panel of |
814 |
+ |
Fig. \ref{vibration}, the large overlap of the vibration spectra of |
815 |
+ |
butanethiol and hexane in the all-atom model, including the C-H |
816 |
+ |
vibration, also suggests high thermal exchange efficiency. The |
817 |
+ |
combination of these two effects produces the drastic interfacial |
818 |
+ |
thermal conductance enhancement in the all-atom model. |
819 |
+ |
|
820 |
+ |
[MAY NEED TO CONVERT TO JPEG] |
821 |
|
\begin{figure} |
822 |
|
\includegraphics[width=\linewidth]{vibration} |
823 |
|
\caption{Vibrational spectra obtained for gold in different |
825 |
|
all-atom model (lower panel).} |
826 |
|
\label{vibration} |
827 |
|
\end{figure} |
523 |
– |
% 600dpi, letter size. too large? |
828 |
|
|
829 |
+ |
[COMPARISON OF TWO G'S; AU SLAB WIDTHS; ETC] |
830 |
+ |
% The results show that the two definitions used for $G$ yield |
831 |
+ |
% comparable values, though $G^\prime$ tends to be smaller. |
832 |
|
|
833 |
+ |
\section{Conclusions} |
834 |
+ |
The NIVS algorithm we developed has been applied to simulations of |
835 |
+ |
Au-butanethiol surfaces with organic solvents. This algorithm allows |
836 |
+ |
effective unphysical thermal flux transferred between the metal and |
837 |
+ |
the liquid phase. With the flux applied, we were able to measure the |
838 |
+ |
corresponding thermal gradient and to obtain interfacial thermal |
839 |
+ |
conductivities. Our simulations have seen significant conductance |
840 |
+ |
enhancement with the presence of capping agent, compared to the bare |
841 |
+ |
gold/liquid interfaces. The acoustic impedance mismatch between the |
842 |
+ |
metal and the liquid phase is effectively eliminated by proper capping |
843 |
+ |
agent. Furthermore, the coverage precentage of the capping agent plays |
844 |
+ |
an important role in the interfacial thermal transport process. |
845 |
+ |
|
846 |
+ |
Our measurement results, particularly of the UA models, agree with |
847 |
+ |
available experimental data. This indicates that our force field |
848 |
+ |
parameters have a nice description of the interactions between the |
849 |
+ |
particles at the interfaces. AA models tend to overestimate the |
850 |
+ |
interfacial thermal conductance in that the classically treated C-H |
851 |
+ |
vibration would be overly sampled. Compared to the AA models, the UA |
852 |
+ |
models have higher computational efficiency with satisfactory |
853 |
+ |
accuracy, and thus are preferable in interfacial thermal transport |
854 |
+ |
modelings. |
855 |
+ |
|
856 |
+ |
Vlugt {\it et al.} has investigated the surface thiol structures for |
857 |
+ |
nanocrystal gold and pointed out that they differs from those of the |
858 |
+ |
Au(111) surface\cite{vlugt:cpc2007154}. This difference might lead to |
859 |
+ |
change of interfacial thermal transport behavior as well. To |
860 |
+ |
investigate this problem, an effective means to introduce thermal flux |
861 |
+ |
and measure the corresponding thermal gradient is desirable for |
862 |
+ |
simulating structures with spherical symmetry. |
863 |
+ |
|
864 |
+ |
|
865 |
|
\section{Acknowledgments} |
866 |
|
Support for this project was provided by the National Science |
867 |
|
Foundation under grant CHE-0848243. Computational time was provided by |
868 |
|
the Center for Research Computing (CRC) at the University of Notre |
869 |
< |
Dame. \newpage |
869 |
> |
Dame. \newpage |
870 |
|
|
871 |
|
\bibliography{interfacial} |
872 |
|
|