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\begin{document} |
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|
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\begin{doublespace} |
45 |
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|
46 |
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\begin{abstract} |
47 |
< |
The abstract version 2 |
47 |
> |
|
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 |
|
|
67 |
|
\newpage |
73 |
|
%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%% |
74 |
|
|
75 |
|
\section{Introduction} |
76 |
+ |
Interfacial thermal conductance is extensively studied both |
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 |
< |
The intro. |
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 alkylthiol 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 comparatively 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 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 the phenomena was investigated. |
135 |
> |
|
136 |
> |
[MAY ADD WHY STUDY AU-THIOL SURFACE; CITE SHAOYI JIANG] |
137 |
> |
|
138 |
> |
\section{Methodology} |
139 |
> |
\subsection{Imposd-Flux Methods in MD Simulations} |
140 |
> |
[CF. CAHILL] |
141 |
> |
For systems with low interfacial conductivity one must have a method |
142 |
> |
capable of generating relatively small fluxes, compared to those |
143 |
> |
required for bulk conductivity. This requirement makes the calculation |
144 |
> |
even more difficult for those slowly-converging equilibrium |
145 |
> |
methods\cite{Viscardy:2007lq}. |
146 |
> |
Forward methods impose gradient, but in interfacial conditions it is |
147 |
> |
not clear what behavior to impose at the boundary... |
148 |
> |
Imposed-flux reverse non-equilibrium |
149 |
> |
methods\cite{MullerPlathe:1997xw} have the flux set {\it a priori} and |
150 |
> |
the thermal response becomes easier to |
151 |
> |
measure than the flux. Although M\"{u}ller-Plathe's original momentum |
152 |
> |
swapping approach can be used for exchanging energy between particles |
153 |
> |
of different identity, the kinetic energy transfer efficiency is |
154 |
> |
affected by the mass difference between the particles, which limits |
155 |
> |
its application on heterogeneous interfacial systems. |
156 |
> |
|
157 |
> |
The non-isotropic velocity scaling (NIVS)\cite{kuang:164101} approach to |
158 |
> |
non-equilibrium MD simulations is able to impose a wide range of |
159 |
> |
kinetic energy fluxes without obvious perturbation to the velocity |
160 |
> |
distributions of the simulated systems. Furthermore, this approach has |
161 |
> |
the advantage in heterogeneous interfaces in that kinetic energy flux |
162 |
> |
can be applied between regions of particles of arbitary identity, and |
163 |
> |
the flux will not be restricted by difference in particle mass. |
164 |
> |
|
165 |
> |
The NIVS algorithm scales the velocity vectors in two separate regions |
166 |
> |
of a simulation system with respective diagonal scaling matricies. To |
167 |
> |
determine these scaling factors in the matricies, a set of equations |
168 |
> |
including linear momentum conservation and kinetic energy conservation |
169 |
> |
constraints and target energy flux satisfaction is solved. With the |
170 |
> |
scaling operation applied to the system in a set frequency, bulk |
171 |
> |
temperature gradients can be easily established, and these can be used |
172 |
> |
for computing thermal conductivities. The NIVS algorithm conserves |
173 |
> |
momenta and energy and does not depend on an external thermostat. |
174 |
> |
|
175 |
> |
\subsection{Defining Interfacial Thermal Conductivity $G$} |
176 |
> |
Given a system with thermal gradients and the corresponding thermal |
177 |
> |
flux, for interfaces with a relatively low interfacial conductance, |
178 |
> |
the bulk regions on either side of an interface rapidly come to a |
179 |
> |
state in which the two phases have relatively homogeneous (but |
180 |
> |
distinct) temperatures. The interfacial thermal conductivity $G$ can |
181 |
> |
therefore be approximated as: |
182 |
> |
\begin{equation} |
183 |
> |
G = \frac{E_{total}}{2 t L_x L_y \left( \langle T_\mathrm{hot}\rangle - |
184 |
> |
\langle T_\mathrm{cold}\rangle \right)} |
185 |
> |
\label{lowG} |
186 |
> |
\end{equation} |
187 |
> |
where ${E_{total}}$ is the imposed non-physical kinetic energy |
188 |
> |
transfer and ${\langle T_\mathrm{hot}\rangle}$ and ${\langle |
189 |
> |
T_\mathrm{cold}\rangle}$ are the average observed temperature of the |
190 |
> |
two separated phases. |
191 |
> |
|
192 |
> |
When the interfacial conductance is {\it not} small, there are two |
193 |
> |
ways to define $G$. |
194 |
> |
|
195 |
> |
One way is to assume the temperature is discrete on the two sides of |
196 |
> |
the interface. $G$ can be calculated using the applied thermal flux |
197 |
> |
$J$ and the maximum temperature difference measured along the thermal |
198 |
> |
gradient max($\Delta T$), which occurs at the Gibbs deviding surface |
199 |
> |
(Figure \ref{demoPic}): |
200 |
> |
\begin{equation} |
201 |
> |
G=\frac{J}{\Delta T} |
202 |
> |
\label{discreteG} |
203 |
> |
\end{equation} |
204 |
> |
|
205 |
> |
\begin{figure} |
206 |
> |
\includegraphics[width=\linewidth]{method} |
207 |
> |
\caption{Interfacial conductance can be calculated by applying an |
208 |
> |
(unphysical) kinetic energy flux between two slabs, one located |
209 |
> |
within the metal and another on the edge of the periodic box. The |
210 |
> |
system responds by forming a thermal response or a gradient. In |
211 |
> |
bulk liquids, this gradient typically has a single slope, but in |
212 |
> |
interfacial systems, there are distinct thermal conductivity |
213 |
> |
domains. The interfacial conductance, $G$ is found by measuring the |
214 |
> |
temperature gap at the Gibbs dividing surface, or by using second |
215 |
> |
derivatives of the thermal profile.} |
216 |
> |
\label{demoPic} |
217 |
> |
\end{figure} |
218 |
> |
|
219 |
> |
The other approach is to assume a continuous temperature profile along |
220 |
> |
the thermal gradient axis (e.g. $z$) and define $G$ at the point where |
221 |
> |
the magnitude of thermal conductivity $\lambda$ change reach its |
222 |
> |
maximum, given that $\lambda$ is well-defined throughout the space: |
223 |
> |
\begin{equation} |
224 |
> |
G^\prime = \Big|\frac{\partial\lambda}{\partial z}\Big| |
225 |
> |
= \Big|\frac{\partial}{\partial z}\left(-J_z\Big/ |
226 |
> |
\left(\frac{\partial T}{\partial z}\right)\right)\Big| |
227 |
> |
= |J_z|\Big|\frac{\partial^2 T}{\partial z^2}\Big| |
228 |
> |
\Big/\left(\frac{\partial T}{\partial z}\right)^2 |
229 |
> |
\label{derivativeG} |
230 |
> |
\end{equation} |
231 |
> |
|
232 |
> |
With the temperature profile obtained from simulations, one is able to |
233 |
> |
approximate the first and second derivatives of $T$ with finite |
234 |
> |
difference methods and thus calculate $G^\prime$. |
235 |
> |
|
236 |
> |
In what follows, both definitions have been used for calculation and |
237 |
> |
are compared in the results. |
238 |
> |
|
239 |
> |
To compare the above definitions ($G$ and $G^\prime$), we have modeled |
240 |
> |
a metal slab with its (111) surfaces perpendicular to the $z$-axis of |
241 |
> |
our simulation cells. Both with and without capping agents on the |
242 |
> |
surfaces, the metal slab is solvated with simple organic solvents, as |
243 |
> |
illustrated in Figure \ref{gradT}. |
244 |
> |
|
245 |
> |
With the simulation cell described above, we are able to equilibrate |
246 |
> |
the system and impose an unphysical thermal flux between the liquid |
247 |
> |
and the metal phase using the NIVS algorithm. By periodically applying |
248 |
> |
the unphysical flux, we are able to obtain a temperature profile and |
249 |
> |
its spatial derivatives. These quantities enable the evaluation of the |
250 |
> |
interfacial thermal conductance of a surface. Figure \ref{gradT} is an |
251 |
> |
example of how an applied thermal flux can be used to obtain the 1st |
252 |
> |
and 2nd derivatives of the temperature profile. |
253 |
> |
|
254 |
> |
\begin{figure} |
255 |
> |
\includegraphics[width=\linewidth]{gradT} |
256 |
> |
\caption{A sample of Au-butanethiol/hexane interfacial system and the |
257 |
> |
temperature profile after a kinetic energy flux is imposed to |
258 |
> |
it. The 1st and 2nd derivatives of the temperature profile can be |
259 |
> |
obtained with finite difference approximation (lower panel).} |
260 |
> |
\label{gradT} |
261 |
> |
\end{figure} |
262 |
> |
|
263 |
> |
\section{Computational Details} |
264 |
> |
\subsection{Simulation Protocol} |
265 |
> |
The NIVS algorithm has been implemented in our MD simulation code, |
266 |
> |
OpenMD\cite{Meineke:2005gd,openmd}, and was used for our |
267 |
> |
simulations. Different metal slab thickness (layer numbers of Au) was |
268 |
> |
simulated. Metal slabs were first equilibrated under atmospheric |
269 |
> |
pressure (1 atm) and a desired temperature (e.g. 200K). After |
270 |
> |
equilibration, butanethiol capping agents were placed at three-fold |
271 |
> |
hollow sites on the Au(111) surfaces. These sites could be either a |
272 |
> |
{\it fcc} or {\it hcp} site. However, Hase {\it et al.} found that |
273 |
> |
they are equivalent in a heat transfer process\cite{hase:2010}, so |
274 |
> |
they are not distinguished in our study. The maximum butanethiol |
275 |
> |
capacity on Au surface is $1/3$ of the total number of surface Au |
276 |
> |
atoms, and the packing forms a $(\sqrt{3}\times\sqrt{3})R30^\circ$ |
277 |
> |
structure[CITE PORTER]. |
278 |
> |
A series of different coverages was derived by evenly eliminating |
279 |
> |
butanethiols on the surfaces, and was investigated in order to study |
280 |
> |
the relation between coverage and interfacial conductance. |
281 |
> |
|
282 |
> |
The capping agent molecules were allowed to migrate during the |
283 |
> |
simulations. They distributed themselves uniformly and sampled a |
284 |
> |
number of three-fold sites throughout out study. Therefore, the |
285 |
> |
initial configuration would not noticeably affect the sampling of a |
286 |
> |
variety of configurations of the same coverage, and the final |
287 |
> |
conductance measurement would be an average effect of these |
288 |
> |
configurations explored in the simulations. [MAY NEED SNAPSHOTS] |
289 |
|
|
290 |
+ |
After the modified Au-butanethiol surface systems were equilibrated |
291 |
+ |
under canonical ensemble, organic solvent molecules were packed in the |
292 |
+ |
previously empty part of the simulation cells\cite{packmol}. Two |
293 |
+ |
solvents were investigated, one which has little vibrational overlap |
294 |
+ |
with the alkanethiol and a planar shape (toluene), and one which has |
295 |
+ |
similar vibrational frequencies and chain-like shape ({\it n}-hexane). |
296 |
+ |
|
297 |
+ |
The space filled by solvent molecules, i.e. the gap between |
298 |
+ |
periodically repeated Au-butanethiol surfaces should be carefully |
299 |
+ |
chosen. A very long length scale for the thermal gradient axis ($z$) |
300 |
+ |
may cause excessively hot or cold temperatures in the middle of the |
301 |
+ |
solvent region and lead to undesired phenomena such as solvent boiling |
302 |
+ |
or freezing when a thermal flux is applied. Conversely, too few |
303 |
+ |
solvent molecules would change the normal behavior of the liquid |
304 |
+ |
phase. Therefore, our $N_{solvent}$ values were chosen to ensure that |
305 |
+ |
these extreme cases did not happen to our simulations. And the |
306 |
+ |
corresponding spacing is usually $35[DOUBLE CHECK] \sim 75$\AA. |
307 |
+ |
|
308 |
+ |
The initial configurations generated are further equilibrated with the |
309 |
+ |
$x$ and $y$ dimensions fixed, only allowing length scale change in $z$ |
310 |
+ |
dimension. This is to ensure that the equilibration of liquid phase |
311 |
+ |
does not affect the metal crystal structure in $x$ and $y$ dimensions. |
312 |
+ |
To investigate this effect, comparisons were made with simulations |
313 |
+ |
that allow changes of $L_x$ and $L_y$ during NPT equilibration, and |
314 |
+ |
the results are shown in later sections. After ensuring the liquid |
315 |
+ |
phase reaches equilibrium at atmospheric pressure (1 atm), further |
316 |
+ |
equilibration are followed under NVT and then NVE ensembles. |
317 |
+ |
|
318 |
+ |
After the systems reach equilibrium, NIVS is implemented to impose a |
319 |
+ |
periodic unphysical thermal flux between the metal and the liquid |
320 |
+ |
phase. Most of our simulations are under an average temperature of |
321 |
+ |
$\sim$200K. Therefore, this flux usually comes from the metal to the |
322 |
+ |
liquid so that the liquid has a higher temperature and would not |
323 |
+ |
freeze due to excessively low temperature. After this induced |
324 |
+ |
temperature gradient is stablized, the temperature profile of the |
325 |
+ |
simulation cell is recorded. To do this, the simulation cell is |
326 |
+ |
devided evenly into $N$ slabs along the $z$-axis and $N$ is maximized |
327 |
+ |
for highest possible spatial resolution but not too many to have some |
328 |
+ |
slabs empty most of the time. The average temperatures of each slab |
329 |
+ |
are recorded for 1$\sim$2 ns. When the slab width $d$ of each slab is |
330 |
+ |
the same, the derivatives of $T$ with respect to slab number $n$ can |
331 |
+ |
be directly used for $G^\prime$ calculations: |
332 |
+ |
\begin{equation} |
333 |
+ |
G^\prime = |J_z|\Big|\frac{\partial^2 T}{\partial z^2}\Big| |
334 |
+ |
\Big/\left(\frac{\partial T}{\partial z}\right)^2 |
335 |
+ |
= |J_z|\Big|\frac{1}{d^2}\frac{\partial^2 T}{\partial n^2}\Big| |
336 |
+ |
\Big/\left(\frac{1}{d}\frac{\partial T}{\partial n}\right)^2 |
337 |
+ |
= |J_z|\Big|\frac{\partial^2 T}{\partial n^2}\Big| |
338 |
+ |
\Big/\left(\frac{\partial T}{\partial n}\right)^2 |
339 |
+ |
\label{derivativeG2} |
340 |
+ |
\end{equation} |
341 |
+ |
|
342 |
+ |
All of the above simulation procedures use a time step of 1 fs. And |
343 |
+ |
each equilibration / stabilization step usually takes 100 ps, or |
344 |
+ |
longer, if necessary. |
345 |
+ |
|
346 |
+ |
\subsection{Force Field Parameters} |
347 |
+ |
Our simulations include various components. Figure \ref{demoMol} |
348 |
+ |
demonstrates the sites defined for both United-Atom and All-Atom |
349 |
+ |
models of the organic solvent and capping agent molecules in our |
350 |
+ |
simulations. Force field parameter descriptions are needed for |
351 |
+ |
interactions both between the same type of particles and between |
352 |
+ |
particles of different species. |
353 |
+ |
|
354 |
+ |
\begin{figure} |
355 |
+ |
\includegraphics[width=\linewidth]{structures} |
356 |
+ |
\caption{Structures of the capping agent and solvents utilized in |
357 |
+ |
these simulations. The chemically-distinct sites (a-e) are expanded |
358 |
+ |
in terms of constituent atoms for both United Atom (UA) and All Atom |
359 |
+ |
(AA) force fields. Most parameters are from |
360 |
+ |
Refs. \protect\cite{TraPPE-UA.alkanes,TraPPE-UA.alkylbenzenes} (UA) and |
361 |
+ |
\protect\cite{OPLSAA} (AA). Cross-interactions with the Au atoms are given |
362 |
+ |
in Table \ref{MnM}.} |
363 |
+ |
\label{demoMol} |
364 |
+ |
\end{figure} |
365 |
+ |
|
366 |
+ |
The Au-Au interactions in metal lattice slab is described by the |
367 |
+ |
quantum Sutton-Chen (QSC) formulation\cite{PhysRevB.59.3527}. The QSC |
368 |
+ |
potentials include zero-point quantum corrections and are |
369 |
+ |
reparametrized for accurate surface energies compared to the |
370 |
+ |
Sutton-Chen potentials\cite{Chen90}. |
371 |
+ |
|
372 |
+ |
For both solvent molecules, straight chain {\it n}-hexane and aromatic |
373 |
+ |
toluene, United-Atom (UA) and All-Atom (AA) models are used |
374 |
+ |
respectively. The TraPPE-UA |
375 |
+ |
parameters\cite{TraPPE-UA.alkanes,TraPPE-UA.alkylbenzenes} are used |
376 |
+ |
for our UA solvent molecules. In these models, sites are located at |
377 |
+ |
the carbon centers for alkyl groups. Bonding interactions, including |
378 |
+ |
bond stretches and bends and torsions, were used for intra-molecular |
379 |
+ |
sites not separated by more than 3 bonds. Otherwise, for non-bonded |
380 |
+ |
interactions, Lennard-Jones potentials are used. [CHECK CITATION] |
381 |
+ |
|
382 |
+ |
By eliminating explicit hydrogen atoms, these models are simple and |
383 |
+ |
computationally efficient, while maintains good accuracy. However, the |
384 |
+ |
TraPPE-UA for alkanes is known to predict a lower boiling point than |
385 |
+ |
experimental values. Considering that after an unphysical thermal flux |
386 |
+ |
is applied to a system, the temperature of ``hot'' area in the liquid |
387 |
+ |
phase would be significantly higher than the average of the system, to |
388 |
+ |
prevent over heating and boiling of the liquid phase, the average |
389 |
+ |
temperature in our simulations should be much lower than the liquid |
390 |
+ |
boiling point. |
391 |
+ |
|
392 |
+ |
For UA-toluene model, the non-bonded potentials between |
393 |
+ |
inter-molecular sites have a similar Lennard-Jones formulation. For |
394 |
+ |
intra-molecular interactions, considering the stiffness of the benzene |
395 |
+ |
ring, rigid body constraints are applied for further computational |
396 |
+ |
efficiency. All bonds in the benzene ring and between the ring and the |
397 |
+ |
methyl group remain rigid during the progress of simulations. |
398 |
+ |
|
399 |
+ |
Besides the TraPPE-UA models, AA models for both organic solvents are |
400 |
+ |
included in our studies as well. For hexane, the OPLS-AA\cite{OPLSAA} |
401 |
+ |
force field is used. Additional explicit hydrogen sites were |
402 |
+ |
included. Besides bonding and non-bonded site-site interactions, |
403 |
+ |
partial charges and the electrostatic interactions were added to each |
404 |
+ |
CT and HC site. For toluene, the United Force Field developed by |
405 |
+ |
Rapp\'{e} {\it et al.}\cite{doi:10.1021/ja00051a040} is |
406 |
+ |
adopted. Without the rigid body constraints, bonding interactions were |
407 |
+ |
included. For the aromatic ring, improper torsions (inversions) were |
408 |
+ |
added as an extra potential for maintaining the planar shape. |
409 |
+ |
[CHECK CITATION] |
410 |
+ |
|
411 |
+ |
The capping agent in our simulations, the butanethiol molecules can |
412 |
+ |
either use UA or AA model. The TraPPE-UA force fields includes |
413 |
+ |
parameters for thiol molecules\cite{TraPPE-UA.thiols} and are used for |
414 |
+ |
UA butanethiol model in our simulations. The OPLS-AA also provides |
415 |
+ |
parameters for alkyl thiols. However, alkyl thiols adsorbed on Au(111) |
416 |
+ |
surfaces do not have the hydrogen atom bonded to sulfur. To adapt this |
417 |
+ |
change and derive suitable parameters for butanethiol adsorbed on |
418 |
+ |
Au(111) surfaces, we adopt the S parameters from Luedtke and |
419 |
+ |
Landman\cite{landman:1998}[CHECK CITATION] |
420 |
+ |
and modify parameters for its neighbor C |
421 |
+ |
atom for charge balance in the molecule. Note that the model choice |
422 |
+ |
(UA or AA) of capping agent can be different from the |
423 |
+ |
solvent. Regardless of model choice, the force field parameters for |
424 |
+ |
interactions between capping agent and solvent can be derived using |
425 |
+ |
Lorentz-Berthelot Mixing Rule: |
426 |
+ |
\begin{eqnarray} |
427 |
+ |
\sigma_{ij} & = & \frac{1}{2} \left(\sigma_{ii} + \sigma_{jj}\right) \\ |
428 |
+ |
\epsilon_{ij} & = & \sqrt{\epsilon_{ii}\epsilon_{jj}} |
429 |
+ |
\end{eqnarray} |
430 |
+ |
|
431 |
+ |
To describe the interactions between metal Au and non-metal capping |
432 |
+ |
agent and solvent particles, we refer to an adsorption study of alkyl |
433 |
+ |
thiols on gold surfaces by Vlugt {\it et |
434 |
+ |
al.}\cite{vlugt:cpc2007154} They fitted an effective Lennard-Jones |
435 |
+ |
form of potential parameters for the interaction between Au and |
436 |
+ |
pseudo-atoms CH$_x$ and S based on a well-established and widely-used |
437 |
+ |
effective potential of Hautman and Klein\cite{hautman:4994} for the |
438 |
+ |
Au(111) surface. As our simulations require the gold lattice slab to |
439 |
+ |
be non-rigid so that it could accommodate kinetic energy for thermal |
440 |
+ |
transport study purpose, the pair-wise form of potentials is |
441 |
+ |
preferred. |
442 |
+ |
|
443 |
+ |
Besides, the potentials developed from {\it ab initio} calculations by |
444 |
+ |
Leng {\it et al.}\cite{doi:10.1021/jp034405s} are adopted for the |
445 |
+ |
interactions between Au and aromatic C/H atoms in toluene. A set of |
446 |
+ |
pseudo Lennard-Jones parameters were provided for Au in their force |
447 |
+ |
fields. By using the Mixing Rule, this can be used to derive pair-wise |
448 |
+ |
potentials for non-bonded interactions between Au and non-metal sites. |
449 |
+ |
|
450 |
+ |
However, the Lennard-Jones parameters between Au and other types of |
451 |
+ |
particles, such as All-Atom normal alkanes in our simulations are not |
452 |
+ |
yet well-established. For these interactions, we attempt to derive |
453 |
+ |
their parameters using the Mixing Rule. To do this, Au pseudo |
454 |
+ |
Lennard-Jones parameters for ``Metal-non-Metal'' (MnM) interactions |
455 |
+ |
were first extracted from the Au-CH$_x$ parameters by applying the |
456 |
+ |
Mixing Rule reversely. Table \ref{MnM} summarizes these ``MnM'' |
457 |
+ |
parameters in our simulations. |
458 |
+ |
|
459 |
+ |
\begin{table*} |
460 |
+ |
\begin{minipage}{\linewidth} |
461 |
+ |
\begin{center} |
462 |
+ |
\caption{Non-bonded interaction parameters (including cross |
463 |
+ |
interactions with Au atoms) for both force fields used in this |
464 |
+ |
work.} |
465 |
+ |
\begin{tabular}{lllllll} |
466 |
+ |
\hline\hline |
467 |
+ |
& Site & $\sigma_{ii}$ & $\epsilon_{ii}$ & $q_i$ & |
468 |
+ |
$\sigma_{Au-i}$ & $\epsilon_{Au-i}$ \\ |
469 |
+ |
& & (\AA) & (kcal/mol) & ($e$) & (\AA) & (kcal/mol) \\ |
470 |
+ |
\hline |
471 |
+ |
United Atom (UA) |
472 |
+ |
&CH3 & 3.75 & 0.1947 & - & 3.54 & 0.2146 \\ |
473 |
+ |
&CH2 & 3.95 & 0.0914 & - & 3.54 & 0.1749 \\ |
474 |
+ |
&CHar & 3.695 & 0.1003 & - & 3.4625 & 0.1680 \\ |
475 |
+ |
&CRar & 3.88 & 0.04173 & - & 3.555 & 0.1604 \\ |
476 |
+ |
\hline |
477 |
+ |
All Atom (AA) |
478 |
+ |
&CT3 & 3.50 & 0.066 & -0.18 & 3.365 & 0.1373 \\ |
479 |
+ |
&CT2 & 3.50 & 0.066 & -0.12 & 3.365 & 0.1373 \\ |
480 |
+ |
&CTT & 3.50 & 0.066 & -0.065 & 3.365 & 0.1373 \\ |
481 |
+ |
&HC & 2.50 & 0.030 & 0.06 & 2.865 & 0.09256 \\ |
482 |
+ |
&CA & 3.55 & 0.070 & -0.115 & 3.173 & 0.0640 \\ |
483 |
+ |
&HA & 2.42 & 0.030 & 0.115 & 2.746 & 0.0414 \\ |
484 |
+ |
\hline |
485 |
+ |
Both UA and AA |
486 |
+ |
& S & 4.45 & 0.25 & - & 2.40 & 8.465 \\ |
487 |
+ |
\hline\hline |
488 |
+ |
\end{tabular} |
489 |
+ |
\label{MnM} |
490 |
+ |
\end{center} |
491 |
+ |
\end{minipage} |
492 |
+ |
\end{table*} |
493 |
+ |
|
494 |
+ |
\subsection{Vibrational Spectrum} |
495 |
+ |
To investigate the mechanism of interfacial thermal conductance, the |
496 |
+ |
vibrational spectrum is utilized as a complementary tool. Vibrational |
497 |
+ |
spectra were taken for individual components in different |
498 |
+ |
simulations. To obtain these spectra, simulations were run after |
499 |
+ |
equilibration, in the NVE ensemble. Snapshots of configurations were |
500 |
+ |
collected at a frequency that is higher than that of the fastest |
501 |
+ |
vibrations occuring in the simulations. With these configurations, the |
502 |
+ |
velocity auto-correlation functions can be computed: |
503 |
+ |
\begin{equation} |
504 |
+ |
C_A (t) = \langle\vec{v}_A (t)\cdot\vec{v}_A (0)\rangle |
505 |
+ |
\label{vCorr} |
506 |
+ |
\end{equation} |
507 |
+ |
|
508 |
+ |
Followed by Fourier transforms, the power spectrum can be constructed: |
509 |
+ |
\begin{equation} |
510 |
+ |
\hat{f}(\omega) = \int_{-\infty}^{\infty} C_A (t) e^{-2\pi it\omega}\,dt |
511 |
+ |
\label{fourier} |
512 |
+ |
\end{equation} |
513 |
+ |
|
514 |
+ |
\section{Results and Discussions} |
515 |
+ |
In what follows, how the parameters and protocol of simulations would |
516 |
+ |
affect the measurement of $G$'s is first discussed. With a reliable |
517 |
+ |
protocol and set of parameters, the influence of capping agent |
518 |
+ |
coverage on thermal conductance is investigated. Besides, different |
519 |
+ |
force field models for both solvents and selected deuterated models |
520 |
+ |
were tested and compared. Finally, a summary of the role of capping |
521 |
+ |
agent in the interfacial thermal transport process is given. |
522 |
+ |
|
523 |
+ |
\subsection{How Simulation Parameters Affects $G$} |
524 |
+ |
We have varied our protocol or other parameters of the simulations in |
525 |
+ |
order to investigate how these factors would affect the measurement of |
526 |
+ |
$G$'s. It turned out that while some of these parameters would not |
527 |
+ |
affect the results substantially, some other changes to the |
528 |
+ |
simulations would have a significant impact on the measurement |
529 |
+ |
results. |
530 |
+ |
|
531 |
+ |
In some of our simulations, we allowed $L_x$ and $L_y$ to change |
532 |
+ |
during equilibrating the liquid phase. Due to the stiffness of the |
533 |
+ |
crystalline Au structure, $L_x$ and $L_y$ would not change noticeably |
534 |
+ |
after equilibration. Although $L_z$ could fluctuate $\sim$1\% after a |
535 |
+ |
system is fully equilibrated in the NPT ensemble, this fluctuation, as |
536 |
+ |
well as those of $L_x$ and $L_y$ (which is significantly smaller), |
537 |
+ |
would not be magnified on the calculated $G$'s, as shown in Table |
538 |
+ |
\ref{AuThiolHexaneUA}. This insensivity to $L_i$ fluctuations allows |
539 |
+ |
reliable measurement of $G$'s without the necessity of extremely |
540 |
+ |
cautious equilibration process. |
541 |
+ |
|
542 |
+ |
As stated in our computational details, the spacing filled with |
543 |
+ |
solvent molecules can be chosen within a range. This allows some |
544 |
+ |
change of solvent molecule numbers for the same Au-butanethiol |
545 |
+ |
surfaces. We did this study on our Au-butanethiol/hexane |
546 |
+ |
simulations. Nevertheless, the results obtained from systems of |
547 |
+ |
different $N_{hexane}$ did not indicate that the measurement of $G$ is |
548 |
+ |
susceptible to this parameter. For computational efficiency concern, |
549 |
+ |
smaller system size would be preferable, given that the liquid phase |
550 |
+ |
structure is not affected. |
551 |
+ |
|
552 |
+ |
Our NIVS algorithm allows change of unphysical thermal flux both in |
553 |
+ |
direction and in quantity. This feature extends our investigation of |
554 |
+ |
interfacial thermal conductance. However, the magnitude of this |
555 |
+ |
thermal flux is not arbitary if one aims to obtain a stable and |
556 |
+ |
reliable thermal gradient. A temperature profile would be |
557 |
+ |
substantially affected by noise when $|J_z|$ has a much too low |
558 |
+ |
magnitude; while an excessively large $|J_z|$ that overwhelms the |
559 |
+ |
conductance capacity of the interface would prevent a thermal gradient |
560 |
+ |
to reach a stablized steady state. NIVS has the advantage of allowing |
561 |
+ |
$J$ to vary in a wide range such that the optimal flux range for $G$ |
562 |
+ |
measurement can generally be simulated by the algorithm. Within the |
563 |
+ |
optimal range, we were able to study how $G$ would change according to |
564 |
+ |
the thermal flux across the interface. For our simulations, we denote |
565 |
+ |
$J_z$ to be positive when the physical thermal flux is from the liquid |
566 |
+ |
to metal, and negative vice versa. The $G$'s measured under different |
567 |
+ |
$J_z$ is listed in Table \ref{AuThiolHexaneUA} and |
568 |
+ |
\ref{AuThiolToluene}. These results do not suggest that $G$ is |
569 |
+ |
dependent on $J_z$ within this flux range. The linear response of flux |
570 |
+ |
to thermal gradient simplifies our investigations in that we can rely |
571 |
+ |
on $G$ measurement with only a couple $J_z$'s and do not need to test |
572 |
+ |
a large series of fluxes. |
573 |
+ |
|
574 |
+ |
\begin{table*} |
575 |
+ |
\begin{minipage}{\linewidth} |
576 |
+ |
\begin{center} |
577 |
+ |
\caption{Computed interfacial thermal conductivity ($G$ and |
578 |
+ |
$G^\prime$) values for the 100\% covered Au-butanethiol/hexane |
579 |
+ |
interfaces with UA model and different hexane molecule numbers |
580 |
+ |
at different temperatures using a range of energy |
581 |
+ |
fluxes. Error estimates indicated in parenthesis.} |
582 |
+ |
|
583 |
+ |
\begin{tabular}{ccccccc} |
584 |
+ |
\hline\hline |
585 |
+ |
$\langle T\rangle$ & $N_{hexane}$ & Fixed & $\rho_{hexane}$ & |
586 |
+ |
$J_z$ & $G$ & $G^\prime$ \\ |
587 |
+ |
(K) & & $L_x$ \& $L_y$? & (g/cm$^3$) & (GW/m$^2$) & |
588 |
+ |
\multicolumn{2}{c}{(MW/m$^2$/K)} \\ |
589 |
+ |
\hline |
590 |
+ |
200 & 266 & No & 0.672 & -0.96 & 102(3) & 80.0(0.8) \\ |
591 |
+ |
& 200 & Yes & 0.694 & 1.92 & 129(11) & 87.3(0.3) \\ |
592 |
+ |
& & Yes & 0.672 & 1.93 & 131(16) & 78(13) \\ |
593 |
+ |
& & No & 0.688 & 0.96 & 125(16) & 90.2(15) \\ |
594 |
+ |
& & & & 1.91 & 139(10) & 101(10) \\ |
595 |
+ |
& & & & 2.83 & 141(6) & 89.9(9.8) \\ |
596 |
+ |
& 166 & Yes & 0.679 & 0.97 & 115(19) & 69(18) \\ |
597 |
+ |
& & & & 1.94 & 125(9) & 87.1(0.2) \\ |
598 |
+ |
& & No & 0.681 & 0.97 & 141(30) & 78(22) \\ |
599 |
+ |
& & & & 1.92 & 138(4) & 98.9(9.5) \\ |
600 |
+ |
\hline |
601 |
+ |
250 & 200 & No & 0.560 & 0.96 & 75(10) & 61.8(7.3) \\ |
602 |
+ |
& & & & -0.95 & 49.4(0.3) & 45.7(2.1) \\ |
603 |
+ |
& 166 & Yes & 0.570 & 0.98 & 79.0(3.5) & 62.9(3.0) \\ |
604 |
+ |
& & No & 0.569 & 0.97 & 80.3(0.6) & 67(11) \\ |
605 |
+ |
& & & & 1.44 & 76.2(5.0) & 64.8(3.8) \\ |
606 |
+ |
& & & & -0.95 & 56.4(2.5) & 54.4(1.1) \\ |
607 |
+ |
& & & & -1.85 & 47.8(1.1) & 53.5(1.5) \\ |
608 |
+ |
\hline\hline |
609 |
+ |
\end{tabular} |
610 |
+ |
\label{AuThiolHexaneUA} |
611 |
+ |
\end{center} |
612 |
+ |
\end{minipage} |
613 |
+ |
\end{table*} |
614 |
+ |
|
615 |
+ |
Furthermore, we also attempted to increase system average temperatures |
616 |
+ |
to above 200K. These simulations are first equilibrated in the NPT |
617 |
+ |
ensemble under normal pressure. As stated above, the TraPPE-UA model |
618 |
+ |
for hexane tends to predict a lower boiling point. In our simulations, |
619 |
+ |
hexane had diffculty to remain in liquid phase when NPT equilibration |
620 |
+ |
temperature is higher than 250K. Additionally, the equilibrated liquid |
621 |
+ |
hexane density under 250K becomes lower than experimental value. This |
622 |
+ |
expanded liquid phase leads to lower contact between hexane and |
623 |
+ |
butanethiol as well.[MAY NEED SLAB DENSITY FIGURE] |
624 |
+ |
And this reduced contact would |
625 |
+ |
probably be accountable for a lower interfacial thermal conductance, |
626 |
+ |
as shown in Table \ref{AuThiolHexaneUA}. |
627 |
+ |
|
628 |
+ |
A similar study for TraPPE-UA toluene agrees with the above result as |
629 |
+ |
well. Having a higher boiling point, toluene tends to remain liquid in |
630 |
+ |
our simulations even equilibrated under 300K in NPT |
631 |
+ |
ensembles. Furthermore, the expansion of the toluene liquid phase is |
632 |
+ |
not as significant as that of the hexane. This prevents severe |
633 |
+ |
decrease of liquid-capping agent contact and the results (Table |
634 |
+ |
\ref{AuThiolToluene}) show only a slightly decreased interface |
635 |
+ |
conductance. Therefore, solvent-capping agent contact should play an |
636 |
+ |
important role in the thermal transport process across the interface |
637 |
+ |
in that higher degree of contact could yield increased conductance. |
638 |
+ |
|
639 |
+ |
\begin{table*} |
640 |
+ |
\begin{minipage}{\linewidth} |
641 |
+ |
\begin{center} |
642 |
+ |
\caption{Computed interfacial thermal conductivity ($G$ and |
643 |
+ |
$G^\prime$) values for a 90\% coverage Au-butanethiol/toluene |
644 |
+ |
interface at different temperatures using a range of energy |
645 |
+ |
fluxes. Error estimates indicated in parenthesis.} |
646 |
+ |
|
647 |
+ |
\begin{tabular}{ccccc} |
648 |
+ |
\hline\hline |
649 |
+ |
$\langle T\rangle$ & $\rho_{toluene}$ & $J_z$ & $G$ & $G^\prime$ \\ |
650 |
+ |
(K) & (g/cm$^3$) & (GW/m$^2$) & \multicolumn{2}{c}{(MW/m$^2$/K)} \\ |
651 |
+ |
\hline |
652 |
+ |
200 & 0.933 & 2.15 & 204(12) & 113(12) \\ |
653 |
+ |
& & -1.86 & 180(3) & 135(21) \\ |
654 |
+ |
& & -3.93 & 176(5) & 113(12) \\ |
655 |
+ |
\hline |
656 |
+ |
300 & 0.855 & -1.91 & 143(5) & 125(2) \\ |
657 |
+ |
& & -4.19 & 135(9) & 113(12) \\ |
658 |
+ |
\hline\hline |
659 |
+ |
\end{tabular} |
660 |
+ |
\label{AuThiolToluene} |
661 |
+ |
\end{center} |
662 |
+ |
\end{minipage} |
663 |
+ |
\end{table*} |
664 |
+ |
|
665 |
+ |
Besides lower interfacial thermal conductance, surfaces in relatively |
666 |
+ |
high temperatures are susceptible to reconstructions, when |
667 |
+ |
butanethiols have a full coverage on the Au(111) surface. These |
668 |
+ |
reconstructions include surface Au atoms migrated outward to the S |
669 |
+ |
atom layer, and butanethiol molecules embedded into the original |
670 |
+ |
surface Au layer. The driving force for this behavior is the strong |
671 |
+ |
Au-S interactions in our simulations. And these reconstructions lead |
672 |
+ |
to higher ratio of Au-S attraction and thus is energetically |
673 |
+ |
favorable. Furthermore, this phenomenon agrees with experimental |
674 |
+ |
results\cite{doi:10.1021/j100035a033,doi:10.1021/la026493y}. Vlugt |
675 |
+ |
{\it et al.} had kept their Au(111) slab rigid so that their |
676 |
+ |
simulations can reach 300K without surface reconstructions. Without |
677 |
+ |
this practice, simulating 100\% thiol covered interfaces under higher |
678 |
+ |
temperatures could hardly avoid surface reconstructions. However, our |
679 |
+ |
measurement is based on assuming homogeneity on $x$ and $y$ dimensions |
680 |
+ |
so that measurement of $T$ at particular $z$ would be an effective |
681 |
+ |
average of the particles of the same type. Since surface |
682 |
+ |
reconstructions could eliminate the original $x$ and $y$ dimensional |
683 |
+ |
homogeneity, measurement of $G$ is more difficult to conduct under |
684 |
+ |
higher temperatures. Therefore, most of our measurements are |
685 |
+ |
undertaken at $\langle T\rangle\sim$200K. |
686 |
+ |
|
687 |
+ |
However, when the surface is not completely covered by butanethiols, |
688 |
+ |
the simulated system is more resistent to the reconstruction |
689 |
+ |
above. Our Au-butanethiol/toluene system had the Au(111) surfaces 90\% |
690 |
+ |
covered by butanethiols, but did not see this above phenomena even at |
691 |
+ |
$\langle T\rangle\sim$300K. The empty three-fold sites not occupied by |
692 |
+ |
capping agents could help prevent surface reconstruction in that they |
693 |
+ |
provide other means of capping agent relaxation. It is observed that |
694 |
+ |
butanethiols can migrate to their neighbor empty sites during a |
695 |
+ |
simulation. Therefore, we were able to obtain $G$'s for these |
696 |
+ |
interfaces even at a relatively high temperature without being |
697 |
+ |
affected by surface reconstructions. |
698 |
+ |
|
699 |
+ |
\subsection{Influence of Capping Agent Coverage on $G$} |
700 |
+ |
To investigate the influence of butanethiol coverage on interfacial |
701 |
+ |
thermal conductance, a series of different coverage Au-butanethiol |
702 |
+ |
surfaces is prepared and solvated with various organic |
703 |
+ |
molecules. These systems are then equilibrated and their interfacial |
704 |
+ |
thermal conductivity are measured with our NIVS algorithm. Figure |
705 |
+ |
\ref{coverage} demonstrates the trend of conductance change with |
706 |
+ |
respect to different coverages of butanethiol. To study the isotope |
707 |
+ |
effect in interfacial thermal conductance, deuterated UA-hexane is |
708 |
+ |
included as well. |
709 |
+ |
|
710 |
+ |
\begin{figure} |
711 |
+ |
\includegraphics[width=\linewidth]{coverage} |
712 |
+ |
\caption{Comparison of interfacial thermal conductivity ($G$) values |
713 |
+ |
for the Au-butanethiol/solvent interface with various UA models and |
714 |
+ |
different capping agent coverages at $\langle T\rangle\sim$200K |
715 |
+ |
using certain energy flux respectively.} |
716 |
+ |
\label{coverage} |
717 |
+ |
\end{figure} |
718 |
+ |
|
719 |
+ |
It turned out that with partial covered butanethiol on the Au(111) |
720 |
+ |
surface, the derivative definition for $G^\prime$ |
721 |
+ |
(Eq. \ref{derivativeG}) was difficult to apply, due to the difficulty |
722 |
+ |
in locating the maximum of change of $\lambda$. Instead, the discrete |
723 |
+ |
definition (Eq. \ref{discreteG}) is easier to apply, as the Gibbs |
724 |
+ |
deviding surface can still be well-defined. Therefore, $G$ (not |
725 |
+ |
$G^\prime$) was used for this section. |
726 |
+ |
|
727 |
+ |
From Figure \ref{coverage}, one can see the significance of the |
728 |
+ |
presence of capping agents. Even when a fraction of the Au(111) |
729 |
+ |
surface sites are covered with butanethiols, the conductivity would |
730 |
+ |
see an enhancement by at least a factor of 3. This indicates the |
731 |
+ |
important role cappping agent is playing for thermal transport |
732 |
+ |
phenomena on metal / organic solvent surfaces. |
733 |
+ |
|
734 |
+ |
Interestingly, as one could observe from our results, the maximum |
735 |
+ |
conductance enhancement (largest $G$) happens while the surfaces are |
736 |
+ |
about 75\% covered with butanethiols. This again indicates that |
737 |
+ |
solvent-capping agent contact has an important role of the thermal |
738 |
+ |
transport process. Slightly lower butanethiol coverage allows small |
739 |
+ |
gaps between butanethiols to form. And these gaps could be filled with |
740 |
+ |
solvent molecules, which acts like ``heat conductors'' on the |
741 |
+ |
surface. The higher degree of interaction between these solvent |
742 |
+ |
molecules and capping agents increases the enhancement effect and thus |
743 |
+ |
produces a higher $G$ than densely packed butanethiol arrays. However, |
744 |
+ |
once this maximum conductance enhancement is reached, $G$ decreases |
745 |
+ |
when butanethiol coverage continues to decrease. Each capping agent |
746 |
+ |
molecule reaches its maximum capacity for thermal |
747 |
+ |
conductance. Therefore, even higher solvent-capping agent contact |
748 |
+ |
would not offset this effect. Eventually, when butanethiol coverage |
749 |
+ |
continues to decrease, solvent-capping agent contact actually |
750 |
+ |
decreases with the disappearing of butanethiol molecules. In this |
751 |
+ |
case, $G$ decrease could not be offset but instead accelerated. [NEED |
752 |
+ |
SNAPSHOT SHOWING THE PHENOMENA / SLAB DENSITY ANALYSIS] |
753 |
+ |
|
754 |
+ |
A comparison of the results obtained from differenet organic solvents |
755 |
+ |
can also provide useful information of the interfacial thermal |
756 |
+ |
transport process. The deuterated hexane (UA) results do not appear to |
757 |
+ |
be much different from those of normal hexane (UA), given that |
758 |
+ |
butanethiol (UA) is non-deuterated for both solvents. These UA model |
759 |
+ |
studies, even though eliminating C-H vibration samplings, still have |
760 |
+ |
C-C vibrational frequencies different from each other. However, these |
761 |
+ |
differences in the infrared range do not seem to produce an observable |
762 |
+ |
difference for the results of $G$ (Figure \ref{uahxnua}). |
763 |
+ |
|
764 |
+ |
\begin{figure} |
765 |
+ |
\includegraphics[width=\linewidth]{uahxnua} |
766 |
+ |
\caption{Vibrational spectra obtained for normal (upper) and |
767 |
+ |
deuterated (lower) hexane in Au-butanethiol/hexane |
768 |
+ |
systems. Butanethiol spectra are shown as reference. Both hexane and |
769 |
+ |
butanethiol were using United-Atom models.} |
770 |
+ |
\label{uahxnua} |
771 |
+ |
\end{figure} |
772 |
+ |
|
773 |
+ |
Furthermore, results for rigid body toluene solvent, as well as other |
774 |
+ |
UA-hexane solvents, are reasonable within the general experimental |
775 |
+ |
ranges[CITATIONS]. This suggests that explicit hydrogen might not be a |
776 |
+ |
required factor for modeling thermal transport phenomena of systems |
777 |
+ |
such as Au-thiol/organic solvent. |
778 |
+ |
|
779 |
+ |
However, results for Au-butanethiol/toluene do not show an identical |
780 |
+ |
trend with those for Au-butanethiol/hexane in that $G$ remains at |
781 |
+ |
approximately the same magnitue when butanethiol coverage differs from |
782 |
+ |
25\% to 75\%. This might be rooted in the molecule shape difference |
783 |
+ |
for planar toluene and chain-like {\it n}-hexane. Due to this |
784 |
+ |
difference, toluene molecules have more difficulty in occupying |
785 |
+ |
relatively small gaps among capping agents when their coverage is not |
786 |
+ |
too low. Therefore, the solvent-capping agent contact may keep |
787 |
+ |
increasing until the capping agent coverage reaches a relatively low |
788 |
+ |
level. This becomes an offset for decreasing butanethiol molecules on |
789 |
+ |
its effect to the process of interfacial thermal transport. Thus, one |
790 |
+ |
can see a plateau of $G$ vs. butanethiol coverage in our results. |
791 |
+ |
|
792 |
+ |
\subsection{Influence of Chosen Molecule Model on $G$} |
793 |
+ |
In addition to UA solvent/capping agent models, AA models are included |
794 |
+ |
in our simulations as well. Besides simulations of the same (UA or AA) |
795 |
+ |
model for solvent and capping agent, different models can be applied |
796 |
+ |
to different components. Furthermore, regardless of models chosen, |
797 |
+ |
either the solvent or the capping agent can be deuterated, similar to |
798 |
+ |
the previous section. Table \ref{modelTest} summarizes the results of |
799 |
+ |
these studies. |
800 |
+ |
|
801 |
+ |
\begin{table*} |
802 |
+ |
\begin{minipage}{\linewidth} |
803 |
+ |
\begin{center} |
804 |
+ |
|
805 |
+ |
\caption{Computed interfacial thermal conductivity ($G$ and |
806 |
+ |
$G^\prime$) values for interfaces using various models for |
807 |
+ |
solvent and capping agent (or without capping agent) at |
808 |
+ |
$\langle T\rangle\sim$200K. (D stands for deuterated solvent |
809 |
+ |
or capping agent molecules; ``Avg.'' denotes results that are |
810 |
+ |
averages of simulations under different $J_z$'s. Error |
811 |
+ |
estimates indicated in parenthesis.)} |
812 |
+ |
|
813 |
+ |
\begin{tabular}{llccc} |
814 |
+ |
\hline\hline |
815 |
+ |
Butanethiol model & Solvent & $J_z$ & $G$ & $G^\prime$ \\ |
816 |
+ |
(or bare surface) & model & (GW/m$^2$) & |
817 |
+ |
\multicolumn{2}{c}{(MW/m$^2$/K)} \\ |
818 |
+ |
\hline |
819 |
+ |
UA & UA hexane & Avg. & 131(9) & 87(10) \\ |
820 |
+ |
& UA hexane(D) & 1.95 & 153(5) & 136(13) \\ |
821 |
+ |
& AA hexane & Avg. & 131(6) & 122(10) \\ |
822 |
+ |
& UA toluene & 1.96 & 187(16) & 151(11) \\ |
823 |
+ |
& AA toluene & 1.89 & 200(36) & 149(53) \\ |
824 |
+ |
\hline |
825 |
+ |
AA & UA hexane & 1.94 & 116(9) & 129(8) \\ |
826 |
+ |
& AA hexane & Avg. & 442(14) & 356(31) \\ |
827 |
+ |
& AA hexane(D) & 1.93 & 222(12) & 234(54) \\ |
828 |
+ |
& UA toluene & 1.98 & 125(25) & 97(60) \\ |
829 |
+ |
& AA toluene & 3.79 & 487(56) & 290(42) \\ |
830 |
+ |
\hline |
831 |
+ |
AA(D) & UA hexane & 1.94 & 158(25) & 172(4) \\ |
832 |
+ |
& AA hexane & 1.92 & 243(29) & 191(11) \\ |
833 |
+ |
& AA toluene & 1.93 & 364(36) & 322(67) \\ |
834 |
+ |
\hline |
835 |
+ |
bare & UA hexane & Avg. & 46.5(3.2) & 49.4(4.5) \\ |
836 |
+ |
& UA hexane(D) & 0.98 & 43.9(4.6) & 43.0(2.0) \\ |
837 |
+ |
& AA hexane & 0.96 & 31.0(1.4) & 29.4(1.3) \\ |
838 |
+ |
& UA toluene & 1.99 & 70.1(1.3) & 65.8(0.5) \\ |
839 |
+ |
\hline\hline |
840 |
+ |
\end{tabular} |
841 |
+ |
\label{modelTest} |
842 |
+ |
\end{center} |
843 |
+ |
\end{minipage} |
844 |
+ |
\end{table*} |
845 |
+ |
|
846 |
+ |
To facilitate direct comparison, the same system with differnt models |
847 |
+ |
for different components uses the same length scale for their |
848 |
+ |
simulation cells. Without the presence of capping agent, using |
849 |
+ |
different models for hexane yields similar results for both $G$ and |
850 |
+ |
$G^\prime$, and these two definitions agree with eath other very |
851 |
+ |
well. This indicates very weak interaction between the metal and the |
852 |
+ |
solvent, and is a typical case for acoustic impedance mismatch between |
853 |
+ |
these two phases. |
854 |
+ |
|
855 |
+ |
As for Au(111) surfaces completely covered by butanethiols, the choice |
856 |
+ |
of models for capping agent and solvent could impact the measurement |
857 |
+ |
of $G$ and $G^\prime$ quite significantly. For Au-butanethiol/hexane |
858 |
+ |
interfaces, using AA model for both butanethiol and hexane yields |
859 |
+ |
substantially higher conductivity values than using UA model for at |
860 |
+ |
least one component of the solvent and capping agent, which exceeds |
861 |
+ |
the general range of experimental measurement results. This is |
862 |
+ |
probably due to the classically treated C-H vibrations in the AA |
863 |
+ |
model, which should not be appreciably populated at normal |
864 |
+ |
temperatures. In comparison, once either the hexanes or the |
865 |
+ |
butanethiols are deuterated, one can see a significantly lower $G$ and |
866 |
+ |
$G^\prime$. In either of these cases, the C-H(D) vibrational overlap |
867 |
+ |
between the solvent and the capping agent is removed (Figure |
868 |
+ |
\ref{aahxntln}). Conclusively, the improperly treated C-H vibration in |
869 |
+ |
the AA model produced over-predicted results accordingly. Compared to |
870 |
+ |
the AA model, the UA model yields more reasonable results with higher |
871 |
+ |
computational efficiency. |
872 |
+ |
|
873 |
+ |
\begin{figure} |
874 |
+ |
\includegraphics[width=\linewidth]{aahxntln} |
875 |
+ |
\caption{Spectra obtained for All-Atom model Au-butanethil/solvent |
876 |
+ |
systems. When butanethiol is deuterated (lower left), its |
877 |
+ |
vibrational overlap with hexane would decrease significantly, |
878 |
+ |
compared with normal butanethiol (upper left). However, this |
879 |
+ |
dramatic change does not apply to toluene as much (right).} |
880 |
+ |
\label{aahxntln} |
881 |
+ |
\end{figure} |
882 |
+ |
|
883 |
+ |
However, for Au-butanethiol/toluene interfaces, having the AA |
884 |
+ |
butanethiol deuterated did not yield a significant change in the |
885 |
+ |
measurement results. Compared to the C-H vibrational overlap between |
886 |
+ |
hexane and butanethiol, both of which have alkyl chains, that overlap |
887 |
+ |
between toluene and butanethiol is not so significant and thus does |
888 |
+ |
not have as much contribution to the ``Intramolecular Vibration |
889 |
+ |
Redistribution''[CITE HASE]. Conversely, extra degrees of freedom such |
890 |
+ |
as the C-H vibrations could yield higher heat exchange rate between |
891 |
+ |
these two phases and result in a much higher conductivity. |
892 |
+ |
|
893 |
+ |
Although the QSC model for Au is known to predict an overly low value |
894 |
+ |
for bulk metal gold conductivity\cite{kuang:164101}, our computational |
895 |
+ |
results for $G$ and $G^\prime$ do not seem to be affected by this |
896 |
+ |
drawback of the model for metal. Instead, our results suggest that the |
897 |
+ |
modeling of interfacial thermal transport behavior relies mainly on |
898 |
+ |
the accuracy of the interaction descriptions between components |
899 |
+ |
occupying the interfaces. |
900 |
+ |
|
901 |
+ |
\subsection{Role of Capping Agent in Interfacial Thermal Conductance} |
902 |
+ |
The vibrational spectra for gold slabs in different environments are |
903 |
+ |
shown as in Figure \ref{specAu}. Regardless of the presence of |
904 |
+ |
solvent, the gold surfaces covered by butanethiol molecules, compared |
905 |
+ |
to bare gold surfaces, exhibit an additional peak observed at the |
906 |
+ |
frequency of $\sim$170cm$^{-1}$, which is attributed to the S-Au |
907 |
+ |
bonding vibration. This vibration enables efficient thermal transport |
908 |
+ |
from surface Au layer to the capping agents. Therefore, in our |
909 |
+ |
simulations, the Au/S interfaces do not appear major heat barriers |
910 |
+ |
compared to the butanethiol / solvent interfaces. |
911 |
+ |
|
912 |
+ |
Simultaneously, the vibrational overlap between butanethiol and |
913 |
+ |
organic solvents suggests higher thermal exchange efficiency between |
914 |
+ |
these two components. Even exessively high heat transport was observed |
915 |
+ |
when All-Atom models were used and C-H vibrations were treated |
916 |
+ |
classically. Compared to metal and organic liquid phase, the heat |
917 |
+ |
transfer efficiency between butanethiol and organic solvents is closer |
918 |
+ |
to that within bulk liquid phase. |
919 |
+ |
|
920 |
+ |
As a combinational effects of the above two, butanethiol acts as a |
921 |
+ |
channel to expedite thermal transport process. The acoustic impedance |
922 |
+ |
mismatch between the metal and the liquid phase can be effectively |
923 |
+ |
reduced with the presence of suitable capping agents. |
924 |
+ |
|
925 |
+ |
\begin{figure} |
926 |
+ |
\includegraphics[width=\linewidth]{vibration} |
927 |
+ |
\caption{Vibrational spectra obtained for gold in different |
928 |
+ |
environments.} |
929 |
+ |
\label{specAu} |
930 |
+ |
\end{figure} |
931 |
+ |
|
932 |
+ |
[MAY ADD COMPARISON OF AU SLAB WIDTHS] |
933 |
+ |
|
934 |
+ |
\section{Conclusions} |
935 |
+ |
The NIVS algorithm we developed has been applied to simulations of |
936 |
+ |
Au-butanethiol surfaces with organic solvents. This algorithm allows |
937 |
+ |
effective unphysical thermal flux transferred between the metal and |
938 |
+ |
the liquid phase. With the flux applied, we were able to measure the |
939 |
+ |
corresponding thermal gradient and to obtain interfacial thermal |
940 |
+ |
conductivities. Under steady states, single trajectory simulation |
941 |
+ |
would be enough for accurate measurement. This would be advantageous |
942 |
+ |
compared to transient state simulations, which need multiple |
943 |
+ |
trajectories to produce reliable average results. |
944 |
+ |
|
945 |
+ |
Our simulations have seen significant conductance enhancement with the |
946 |
+ |
presence of capping agent, compared to the bare gold / liquid |
947 |
+ |
interfaces. The acoustic impedance mismatch between the metal and the |
948 |
+ |
liquid phase is effectively eliminated by proper capping |
949 |
+ |
agent. Furthermore, the coverage precentage of the capping agent plays |
950 |
+ |
an important role in the interfacial thermal transport |
951 |
+ |
process. Moderately lower coverages allow higher contact between |
952 |
+ |
capping agent and solvent, and thus could further enhance the heat |
953 |
+ |
transfer process. |
954 |
+ |
|
955 |
+ |
Our measurement results, particularly of the UA models, agree with |
956 |
+ |
available experimental data. This indicates that our force field |
957 |
+ |
parameters have a nice description of the interactions between the |
958 |
+ |
particles at the interfaces. AA models tend to overestimate the |
959 |
+ |
interfacial thermal conductance in that the classically treated C-H |
960 |
+ |
vibration would be overly sampled. Compared to the AA models, the UA |
961 |
+ |
models have higher computational efficiency with satisfactory |
962 |
+ |
accuracy, and thus are preferable in interfacial thermal transport |
963 |
+ |
modelings. Of the two definitions for $G$, the discrete form |
964 |
+ |
(Eq. \ref{discreteG}) was easier to use and gives out relatively |
965 |
+ |
consistent results, while the derivative form (Eq. \ref{derivativeG}) |
966 |
+ |
is not as versatile. Although $G^\prime$ gives out comparable results |
967 |
+ |
and follows similar trend with $G$ when measuring close to fully |
968 |
+ |
covered or bare surfaces, the spatial resolution of $T$ profile is |
969 |
+ |
limited for accurate computation of derivatives data. |
970 |
+ |
|
971 |
+ |
Vlugt {\it et al.} has investigated the surface thiol structures for |
972 |
+ |
nanocrystal gold and pointed out that they differs from those of the |
973 |
+ |
Au(111) surface\cite{vlugt:cpc2007154}. This difference might lead to |
974 |
+ |
change of interfacial thermal transport behavior as well. To |
975 |
+ |
investigate this problem, an effective means to introduce thermal flux |
976 |
+ |
and measure the corresponding thermal gradient is desirable for |
977 |
+ |
simulating structures with spherical symmetry. |
978 |
+ |
|
979 |
|
\section{Acknowledgments} |
980 |
|
Support for this project was provided by the National Science |
981 |
|
Foundation under grant CHE-0848243. Computational time was provided by |
982 |
|
the Center for Research Computing (CRC) at the University of Notre |
983 |
< |
Dame. \newpage |
983 |
> |
Dame. \newpage |
984 |
|
|
985 |
|
\bibliography{interfacial} |
986 |
|
|