44 |
|
\begin{doublespace} |
45 |
|
|
46 |
|
\begin{abstract} |
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 |
< |
|
47 |
> |
With the Non-Isotropic Velocity Scaling (NIVS) approach to Reverse |
48 |
> |
Non-Equilibrium Molecular Dynamics (RNEMD) it is possible to impose |
49 |
> |
an unphysical thermal flux between different regions of |
50 |
> |
inhomogeneous systems such as solid / liquid interfaces. We have |
51 |
> |
applied NIVS to compute the interfacial thermal conductance at a |
52 |
> |
metal / organic solvent interface that has been chemically capped by |
53 |
> |
butanethiol molecules. Our calculations suggest that the acoustic |
54 |
> |
impedance mismatch between the metal and liquid phases is |
55 |
> |
effectively reduced by the capping agents, leading to a greatly |
56 |
> |
enhanced conductivity at the interface. Specifically, the chemical |
57 |
> |
bond between the metal and the capping agent introduces a |
58 |
> |
vibrational overlap that is not present without the capping agent, |
59 |
> |
and the overlap between the vibrational spectra (metal to cap, cap |
60 |
> |
to solvent) provides a mechanism for rapid thermal transport across |
61 |
> |
the interface. Our calculations also suggest that this is a |
62 |
> |
non-monotonic function of the fractional coverage of the surface, as |
63 |
> |
moderate coverages allow convective heat transport of solvent |
64 |
> |
molecules that have been in close contact with the capping agent. |
65 |
|
\end{abstract} |
66 |
|
|
67 |
|
\newpage |
73 |
|
%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%% |
74 |
|
|
75 |
|
\section{Introduction} |
76 |
< |
Due to the importance of heat flow in nanotechnology, interfacial |
77 |
< |
thermal conductance has been studied extensively both experimentally |
78 |
< |
and computationally.\cite{cahill:793} Unlike bulk materials, nanoscale |
79 |
< |
materials have a significant fraction of their atoms at interfaces, |
80 |
< |
and the chemical details of these interfaces govern the heat transfer |
81 |
< |
behavior. Furthermore, the interfaces are |
76 |
> |
Due to the importance of heat flow (and heat removal) in |
77 |
> |
nanotechnology, interfacial thermal conductance has been studied |
78 |
> |
extensively both experimentally and computationally.\cite{cahill:793} |
79 |
> |
Nanoscale materials have a significant fraction of their atoms at |
80 |
> |
interfaces, and the chemical details of these interfaces govern the |
81 |
> |
thermal transport properties. Furthermore, the interfaces are often |
82 |
|
heterogeneous (e.g. solid - liquid), which provides a challenge to |
83 |
< |
traditional methods developed for homogeneous systems. |
83 |
> |
computational methods which have been developed for homogeneous or |
84 |
> |
bulk systems. |
85 |
|
|
86 |
< |
Experimentally, various interfaces have been investigated for their |
87 |
< |
thermal conductance. Cahill and coworkers studied nanoscale thermal |
86 |
> |
Experimentally, the thermal properties of a number of interfaces have |
87 |
> |
been investigated. Cahill and coworkers studied nanoscale thermal |
88 |
|
transport from metal nanoparticle/fluid interfaces, to epitaxial |
89 |
< |
TiN/single crystal oxides interfaces, to hydrophilic and hydrophobic |
89 |
> |
TiN/single crystal oxides interfaces, and hydrophilic and hydrophobic |
90 |
|
interfaces between water and solids with different self-assembled |
91 |
|
monolayers.\cite{Wilson:2002uq,PhysRevB.67.054302,doi:10.1021/jp048375k,PhysRevLett.96.186101} |
92 |
< |
Wang {\it et al.} studied heat transport through |
93 |
< |
long-chain hydrocarbon monolayers on gold substrate at individual |
94 |
< |
molecular level,\cite{Wang10082007} Schmidt {\it et al.} studied the |
95 |
< |
role of CTAB on thermal transport between gold nanorods and |
96 |
< |
solvent,\cite{doi:10.1021/jp8051888} and Juv\'e {\it et al.} studied |
97 |
< |
the cooling dynamics, which is controlled by thermal interface |
98 |
< |
resistence of glass-embedded metal |
92 |
> |
Wang {\it et al.} studied heat transport through long-chain |
93 |
> |
hydrocarbon monolayers on gold substrate at individual molecular |
94 |
> |
level,\cite{Wang10082007} Schmidt {\it et al.} studied the role of |
95 |
> |
cetyltrimethylammonium bromide (CTAB) on the thermal transport between |
96 |
> |
gold nanorods and solvent,\cite{doi:10.1021/jp8051888} and Juv\'e {\it |
97 |
> |
et al.} studied the cooling dynamics, which is controlled by thermal |
98 |
> |
interface resistance of glass-embedded metal |
99 |
|
nanoparticles.\cite{PhysRevB.80.195406} Although interfaces are |
100 |
|
normally considered barriers for heat transport, Alper {\it et al.} |
101 |
|
suggested that specific ligands (capping agents) could completely |
115 |
|
difficult to measure with Equilibrium |
116 |
|
MD\cite{doi:10.1080/0026897031000068578} or forward NEMD simulation |
117 |
|
methods. Therefore, the Reverse NEMD (RNEMD) |
118 |
< |
methods\cite{MullerPlathe:1997xw,kuang:164101} would have the |
119 |
< |
advantage of applying this difficult to measure flux (while measuring |
120 |
< |
the resulting gradient), given that the simulation methods being able |
121 |
< |
to effectively apply an unphysical flux in non-homogeneous systems. |
118 |
> |
methods\cite{MullerPlathe:1997xw,kuang:164101} would be advantageous |
119 |
> |
in that they {\it apply} the difficult to measure quantity (flux), |
120 |
> |
while {\it measuring} the easily-computed quantity (the thermal |
121 |
> |
gradient). This is particularly true for inhomogeneous interfaces |
122 |
> |
where it would not be clear how to apply a gradient {\it a priori}. |
123 |
|
Garde and coworkers\cite{garde:nl2005,garde:PhysRevLett2009} applied |
124 |
|
this approach to various liquid interfaces and studied how thermal |
125 |
< |
conductance (or resistance) is dependent on chemistry details of |
126 |
< |
interfaces, e.g. hydrophobic and hydrophilic aqueous interfaces. |
125 |
> |
conductance (or resistance) is dependent on chemical details of a |
126 |
> |
number of hydrophobic and hydrophilic aqueous interfaces. {\bf And |
127 |
> |
Luo {\it et al.} studied the thermal conductance of Au-SAM-Au |
128 |
> |
junctions using the same approach, with comparison to a constant |
129 |
> |
temperature difference method\cite{Luo20101}. While this latter |
130 |
> |
approach establishes more thermal distributions compared to the |
131 |
> |
former RNEMD methods, it does not guarantee momentum or kinetic |
132 |
> |
energy conservations.} |
133 |
|
|
134 |
|
Recently, we have developed a Non-Isotropic Velocity Scaling (NIVS) |
135 |
|
algorithm for RNEMD simulations\cite{kuang:164101}. This algorithm |
143 |
|
The work presented here deals with the Au(111) surface covered to |
144 |
|
varying degrees by butanethiol, a capping agent with short carbon |
145 |
|
chain, and solvated with organic solvents of different molecular |
146 |
< |
properties. Different models were used for both the capping agent and |
147 |
< |
the solvent force field parameters. Using the NIVS algorithm, the |
148 |
< |
thermal transport across these interfaces was studied and the |
149 |
< |
underlying mechanism for the phenomena was investigated. |
146 |
> |
properties. {\bf To our knowledge, few previous MD inverstigations |
147 |
> |
have been found to address to these systems yet.} Different models |
148 |
> |
were used for both the capping agent and the solvent force field |
149 |
> |
parameters. Using the NIVS algorithm, the thermal transport across |
150 |
> |
these interfaces was studied and the underlying mechanism for the |
151 |
> |
phenomena was investigated. |
152 |
|
|
153 |
|
\section{Methodology} |
154 |
< |
\subsection{Imposd-Flux Methods in MD Simulations} |
154 |
> |
\subsection{Imposed-Flux Methods in MD Simulations} |
155 |
|
Steady state MD simulations have an advantage in that not many |
156 |
|
trajectories are needed to study the relationship between thermal flux |
157 |
|
and thermal gradients. For systems with low interfacial conductance, |
175 |
|
kinetic energy fluxes without obvious perturbation to the velocity |
176 |
|
distributions of the simulated systems. Furthermore, this approach has |
177 |
|
the advantage in heterogeneous interfaces in that kinetic energy flux |
178 |
< |
can be applied between regions of particles of arbitary identity, and |
178 |
> |
can be applied between regions of particles of arbitrary identity, and |
179 |
|
the flux will not be restricted by difference in particle mass. |
180 |
|
|
181 |
|
The NIVS algorithm scales the velocity vectors in two separate regions |
182 |
< |
of a simulation system with respective diagonal scaling matricies. To |
183 |
< |
determine these scaling factors in the matricies, a set of equations |
182 |
> |
of a simulation system with respective diagonal scaling matrices. To |
183 |
> |
determine these scaling factors in the matrices, a set of equations |
184 |
|
including linear momentum conservation and kinetic energy conservation |
185 |
|
constraints and target energy flux satisfaction is solved. With the |
186 |
|
scaling operation applied to the system in a set frequency, bulk |
212 |
|
discrete on the two sides of the interface. $G$ can be calculated |
213 |
|
using the applied thermal flux $J$ and the maximum temperature |
214 |
|
difference measured along the thermal gradient max($\Delta T$), which |
215 |
< |
occurs at the Gibbs deviding surface (Figure \ref{demoPic}). This is |
215 |
> |
occurs at the Gibbs dividing surface (Figure \ref{demoPic}). This is |
216 |
|
known as the Kapitza conductance, which is the inverse of the Kapitza |
217 |
|
resistance. |
218 |
|
\begin{equation} |
225 |
|
\caption{Interfacial conductance can be calculated by applying an |
226 |
|
(unphysical) kinetic energy flux between two slabs, one located |
227 |
|
within the metal and another on the edge of the periodic box. The |
228 |
< |
system responds by forming a thermal response or a gradient. In |
229 |
< |
bulk liquids, this gradient typically has a single slope, but in |
230 |
< |
interfacial systems, there are distinct thermal conductivity |
231 |
< |
domains. The interfacial conductance, $G$ is found by measuring the |
232 |
< |
temperature gap at the Gibbs dividing surface, or by using second |
233 |
< |
derivatives of the thermal profile.} |
228 |
> |
system responds by forming a thermal gradient. In bulk liquids, |
229 |
> |
this gradient typically has a single slope, but in interfacial |
230 |
> |
systems, there are distinct thermal conductivity domains. The |
231 |
> |
interfacial conductance, $G$ is found by measuring the temperature |
232 |
> |
gap at the Gibbs dividing surface, or by using second derivatives of |
233 |
> |
the thermal profile.} |
234 |
|
\label{demoPic} |
235 |
|
\end{figure} |
236 |
|
|
269 |
|
|
270 |
|
\begin{figure} |
271 |
|
\includegraphics[width=\linewidth]{gradT} |
272 |
< |
\caption{A sample of Au-butanethiol/hexane interfacial system and the |
273 |
< |
temperature profile after a kinetic energy flux is imposed to |
274 |
< |
it. The 1st and 2nd derivatives of the temperature profile can be |
275 |
< |
obtained with finite difference approximation (lower panel).} |
272 |
> |
\caption{A sample of Au (111) / butanethiol / hexane interfacial |
273 |
> |
system with the temperature profile after a kinetic energy flux has |
274 |
> |
been imposed. Note that the largest temperature jump in the thermal |
275 |
> |
profile (corresponding to the lowest interfacial conductance) is at |
276 |
> |
the interface between the butanethiol molecules (blue) and the |
277 |
> |
solvent (grey). First and second derivatives of the temperature |
278 |
> |
profile are obtained using a finite difference approximation (lower |
279 |
> |
panel).} |
280 |
|
\label{gradT} |
281 |
|
\end{figure} |
282 |
|
|
323 |
|
solvent molecules would change the normal behavior of the liquid |
324 |
|
phase. Therefore, our $N_{solvent}$ values were chosen to ensure that |
325 |
|
these extreme cases did not happen to our simulations. The spacing |
326 |
< |
between periodic images of the gold interfaces is $45 \sim 75$\AA. |
326 |
> |
between periodic images of the gold interfaces is $45 \sim 75$\AA in |
327 |
> |
our simulations. |
328 |
|
|
329 |
|
The initial configurations generated are further equilibrated with the |
330 |
|
$x$ and $y$ dimensions fixed, only allowing the $z$-length scale to |
342 |
|
$\sim$200K. Therefore, thermal flux usually came from the metal to the |
343 |
|
liquid so that the liquid has a higher temperature and would not |
344 |
|
freeze due to lowered temperatures. After this induced temperature |
345 |
< |
gradient had stablized, the temperature profile of the simulation cell |
346 |
< |
was recorded. To do this, the simulation cell is devided evenly into |
345 |
> |
gradient had stabilized, the temperature profile of the simulation cell |
346 |
> |
was recorded. To do this, the simulation cell is divided evenly into |
347 |
|
$N$ slabs along the $z$-axis. The average temperatures of each slab |
348 |
|
are recorded for 1$\sim$2 ns. When the slab width $d$ of each slab is |
349 |
|
the same, the derivatives of $T$ with respect to slab number $n$ can |
374 |
|
\caption{Structures of the capping agent and solvents utilized in |
375 |
|
these simulations. The chemically-distinct sites (a-e) are expanded |
376 |
|
in terms of constituent atoms for both United Atom (UA) and All Atom |
377 |
< |
(AA) force fields. Most parameters are from |
378 |
< |
Refs. \protect\cite{TraPPE-UA.alkanes,TraPPE-UA.alkylbenzenes,TraPPE-UA.thiols} |
377 |
> |
(AA) force fields. Most parameters are from References |
378 |
> |
\protect\cite{TraPPE-UA.alkanes,TraPPE-UA.alkylbenzenes,TraPPE-UA.thiols} |
379 |
|
(UA) and \protect\cite{OPLSAA} (AA). Cross-interactions with the Au |
380 |
|
atoms are given in Table \ref{MnM}.} |
381 |
|
\label{demoMol} |
399 |
|
|
400 |
|
By eliminating explicit hydrogen atoms, the TraPPE-UA models are |
401 |
|
simple and computationally efficient, while maintaining good accuracy. |
402 |
< |
However, the TraPPE-UA model for alkanes is known to predict a slighly |
402 |
> |
However, the TraPPE-UA model for alkanes is known to predict a slightly |
403 |
|
lower boiling point than experimental values. This is one of the |
404 |
|
reasons we used a lower average temperature (200K) for our |
405 |
|
simulations. If heat is transferred to the liquid phase during the |
518 |
|
|
519 |
|
\begin{figure} |
520 |
|
\includegraphics[width=\linewidth]{coverage} |
521 |
< |
\caption{Comparison of interfacial thermal conductivity ($G$) values |
522 |
< |
for the Au-butanethiol/solvent interface with various UA models and |
523 |
< |
different capping agent coverages at $\langle T\rangle\sim$200K.} |
521 |
> |
\caption{The interfacial thermal conductivity ($G$) has a |
522 |
> |
non-monotonic dependence on the degree of surface capping. This |
523 |
> |
data is for the Au(111) / butanethiol / solvent interface with |
524 |
> |
various UA force fields at $\langle T\rangle \sim $200K.} |
525 |
|
\label{coverage} |
526 |
|
\end{figure} |
527 |
|
|
535 |
|
From Figure \ref{coverage}, one can see the significance of the |
536 |
|
presence of capping agents. When even a small fraction of the Au(111) |
537 |
|
surface sites are covered with butanethiols, the conductivity exhibits |
538 |
< |
an enhancement by at least a factor of 3. Cappping agents are clearly |
538 |
> |
an enhancement by at least a factor of 3. Capping agents are clearly |
539 |
|
playing a major role in thermal transport at metal / organic solvent |
540 |
|
surfaces. |
541 |
|
|
593 |
|
\caption{Computed interfacial thermal conductance ($G$ and |
594 |
|
$G^\prime$) values for interfaces using various models for |
595 |
|
solvent and capping agent (or without capping agent) at |
596 |
< |
$\langle T\rangle\sim$200K. (D stands for deuterated solvent |
597 |
< |
or capping agent molecules; ``Avg.'' denotes results that are |
598 |
< |
averages of simulations under different applied thermal flux values $(J_z)$. Error |
599 |
< |
estimates are indicated in parentheses.)} |
596 |
> |
$\langle T\rangle\sim$200K. Here ``D'' stands for deuterated |
597 |
> |
solvent or capping agent molecules; ``Avg.'' denotes results |
598 |
> |
that are averages of simulations under different applied |
599 |
> |
thermal flux $(J_z)$ values. Error estimates are indicated in |
600 |
> |
parentheses.} |
601 |
|
|
602 |
|
\begin{tabular}{llccc} |
603 |
|
\hline\hline |
644 |
|
phases. |
645 |
|
|
646 |
|
For the fully-covered surfaces, the choice of force field for the |
647 |
< |
capping agent and solvent has a large impact on the calulated values |
647 |
> |
capping agent and solvent has a large impact on the calculated values |
648 |
|
of $G$ and $G^\prime$. The AA thiol to AA solvent conductivities are |
649 |
|
much larger than their UA to UA counterparts, and these values exceed |
650 |
|
the experimental estimates by a large measure. The AA force field |
699 |
|
flow simply by changing the sign of the flux, and thermal gradients |
700 |
|
which would be difficult to obtain experimentally ($5$ K/\AA) can be |
701 |
|
easily simulated. However, the magnitude of the applied flux is not |
702 |
< |
arbitary if one aims to obtain a stable and reliable thermal gradient. |
702 |
> |
arbitrary if one aims to obtain a stable and reliable thermal gradient. |
703 |
|
A temperature gradient can be lost in the noise if $|J_z|$ is too |
704 |
|
small, and excessive $|J_z|$ values can cause phase transitions if the |
705 |
|
extremes of the simulation cell become widely separated in |
724 |
|
\begin{table*} |
725 |
|
\begin{minipage}{\linewidth} |
726 |
|
\begin{center} |
727 |
< |
\caption{Computed interfacial thermal conductivity ($G$ and |
728 |
< |
$G^\prime$) values for the 100\% covered Au-butanethiol/hexane |
729 |
< |
interfaces with UA model and different hexane molecule numbers |
730 |
< |
at different temperatures using a range of energy |
731 |
< |
fluxes. Error estimates indicated in parenthesis.} |
727 |
> |
\caption{In the hexane-solvated interfaces, the system size has |
728 |
> |
little effect on the calculated values for interfacial |
729 |
> |
conductance ($G$ and $G^\prime$), but the direction of heat |
730 |
> |
flow (i.e. the sign of $J_z$) can alter the average |
731 |
> |
temperature of the liquid phase and this can alter the |
732 |
> |
computed conductivity.} |
733 |
|
|
734 |
|
\begin{tabular}{ccccccc} |
735 |
|
\hline\hline |
778 |
|
between the hexane and butanethiol, and this accounts for our |
779 |
|
observation of lower conductance at higher temperatures as shown in |
780 |
|
Table \ref{AuThiolHexaneUA}. In raising the average temperature from |
781 |
< |
200K to 250K, the density drop of ~20\% in the solvent phase leads to |
782 |
< |
a ~65\% drop in the conductance. |
781 |
> |
200K to 250K, the density drop of $\sim$20\% in the solvent phase |
782 |
> |
leads to a $\sim$40\% drop in the conductance. |
783 |
|
|
784 |
|
Similar behavior is observed in the TraPPE-UA model for toluene, |
785 |
|
although this model has better agreement with the experimental |
786 |
|
densities of toluene. The expansion of the toluene liquid phase is |
787 |
|
not as significant as that of the hexane (8.3\% over 100K), and this |
788 |
< |
limits the effect to ~20\% drop in thermal conductivity (Table |
788 |
> |
limits the effect to $\sim$20\% drop in thermal conductivity (Table |
789 |
|
\ref{AuThiolToluene}). |
790 |
|
|
791 |
|
Although we have not mapped out the behavior at a large number of |
797 |
|
\begin{table*} |
798 |
|
\begin{minipage}{\linewidth} |
799 |
|
\begin{center} |
800 |
< |
\caption{Computed interfacial thermal conductivity ($G$ and |
801 |
< |
$G^\prime$) values for a 90\% coverage Au-butanethiol/toluene |
802 |
< |
interface at different temperatures using a range of energy |
803 |
< |
fluxes. Error estimates indicated in parenthesis.} |
800 |
> |
\caption{When toluene is the solvent, the interfacial thermal |
801 |
> |
conductivity is less sensitive to temperature, but again, the |
802 |
> |
direction of the heat flow can alter the solvent temperature |
803 |
> |
and can change the computed conductance values.} |
804 |
|
|
805 |
|
\begin{tabular}{ccccc} |
806 |
|
\hline\hline |
827 |
|
S atom layer, and butanethiol molecules which embed into the surface |
828 |
|
Au layer. The driving force for this behavior is the strong Au-S |
829 |
|
interactions which are modeled here with a deep Lennard-Jones |
830 |
< |
potential. This phenomenon agrees with reconstructions that have beeen |
830 |
> |
potential. This phenomenon agrees with reconstructions that have been |
831 |
|
experimentally |
832 |
|
observed.\cite{doi:10.1021/j100035a033,doi:10.1021/la026493y}. Vlugt |
833 |
|
{\it et al.} kept their Au(111) slab rigid so that their simulations |
840 |
|
|
841 |
|
However, when the surface is not completely covered by butanethiols, |
842 |
|
the simulated system appears to be more resistent to the |
843 |
< |
reconstruction. O ur Au / butanethiol / toluene system had the Au(111) |
843 |
> |
reconstruction. Our Au / butanethiol / toluene system had the Au(111) |
844 |
|
surfaces 90\% covered by butanethiols, but did not see this above |
845 |
|
phenomena even at $\langle T\rangle\sim$300K. That said, we did |
846 |
|
observe butanethiols migrating to neighboring three-fold sites during |
847 |
< |
a simulation. Since the interface persisted in these simulations, |
847 |
> |
a simulation. Since the interface persisted in these simulations, we |
848 |
|
were able to obtain $G$'s for these interfaces even at a relatively |
849 |
|
high temperature without being affected by surface reconstructions. |
850 |
|
|
863 |
|
spectra, simulations were run after equilibration in the |
864 |
|
microcanonical (NVE) ensemble and without a thermal |
865 |
|
gradient. Snapshots of configurations were collected at a frequency |
866 |
< |
that is higher than that of the fastest vibrations occuring in the |
866 |
> |
that is higher than that of the fastest vibrations occurring in the |
867 |
|
simulations. With these configurations, the velocity auto-correlation |
868 |
|
functions can be computed: |
869 |
|
\begin{equation} |
883 |
|
shown as in Figure \ref{specAu}. Regardless of the presence of |
884 |
|
solvent, the gold surfaces which are covered by butanethiol molecules |
885 |
|
exhibit an additional peak observed at a frequency of |
886 |
< |
$\sim$170cm$^{-1}$. We attribute this peak to the S-Au bonding |
886 |
> |
$\sim$165cm$^{-1}$. We attribute this peak to the S-Au bonding |
887 |
|
vibration. This vibration enables efficient thermal coupling of the |
888 |
|
surface Au layer to the capping agents. Therefore, in our simulations, |
889 |
|
the Au / S interfaces do not appear to be the primary barrier to |
890 |
|
thermal transport when compared with the butanethiol / solvent |
891 |
< |
interfaces. |
891 |
> |
interfaces. {\bf This confirms the results from Luo {\it et |
892 |
> |
al.}\cite{Luo20101}, which reported $G$ for Au-SAM junctions |
893 |
> |
generally twice larger than what we have computed for the |
894 |
> |
thiol-liquid interfaces.} |
895 |
|
|
896 |
|
\begin{figure} |
897 |
|
\includegraphics[width=\linewidth]{vibration} |
898 |
< |
\caption{Vibrational power spectra for gold in different solvent |
899 |
< |
environments. The presence of the butanethiol capping molecules |
900 |
< |
adds a vibrational peak at $\sim$170cm$^{-1}$.} |
898 |
> |
\caption{The vibrational power spectrum for thiol-capped gold has an |
899 |
> |
additional vibrational peak at $\sim $165cm$^{-1}$. Bare gold |
900 |
> |
surfaces (both with and without a solvent over-layer) are missing |
901 |
> |
this peak. A similar peak at $\sim $165cm$^{-1}$ also appears in |
902 |
> |
the vibrational power spectrum for the butanethiol capping agents.} |
903 |
|
\label{specAu} |
904 |
|
\end{figure} |
905 |
|
|
906 |
|
Also in this figure, we show the vibrational power spectrum for the |
907 |
|
bound butanethiol molecules, which also exhibits the same |
908 |
< |
$\sim$170cm$^{-1}$ peak. |
908 |
> |
$\sim$165cm$^{-1}$ peak. |
909 |
|
|
910 |
|
\subsection{Overlap of power spectra} |
911 |
|
A comparison of the results obtained from the two different organic |
917 |
|
vibrations were treated classically. The presence of extra degrees of |
918 |
|
freedom in the AA force field yields higher heat exchange rates |
919 |
|
between the two phases and results in a much higher conductivity than |
920 |
< |
in the UA force field. |
920 |
> |
in the UA force field. {\bf Due to the classical models used, this |
921 |
> |
even includes those high frequency modes which should be unpopulated |
922 |
> |
at our relatively low temperatures. This artifact causes high |
923 |
> |
frequency vibrations accountable for thermal transport in classical |
924 |
> |
MD simulations.} |
925 |
|
|
926 |
|
The similarity in the vibrational modes available to solvent and |
927 |
|
capping agent can be reduced by deuterating one of the two components |
966 |
|
|
967 |
|
\begin{figure} |
968 |
|
\includegraphics[width=\linewidth]{uahxnua} |
969 |
< |
\caption{Vibrational spectra obtained for normal (upper) and |
970 |
< |
deuterated (lower) hexane in Au-butanethiol/hexane |
971 |
< |
systems. Butanethiol spectra are shown as reference. Both hexane and |
972 |
< |
butanethiol were using United-Atom models.} |
969 |
> |
\caption{Vibrational power spectra for UA models for the butanethiol |
970 |
> |
and hexane solvent (upper panel) show the high degree of overlap |
971 |
> |
between these two molecules, particularly at lower frequencies. |
972 |
> |
Deuterating a UA model for the solvent (lower panel) does not |
973 |
> |
decouple the two spectra to the same degree as in the AA force |
974 |
> |
field (see Fig \ref{aahxntln}).} |
975 |
|
\label{uahxnua} |
976 |
|
\end{figure} |
977 |
|
|
989 |
|
presence of capping agent, compared with the bare gold / liquid |
990 |
|
interfaces. The acoustic impedance mismatch between the metal and the |
991 |
|
liquid phase is effectively eliminated by a chemically-bonded capping |
992 |
< |
agent. Furthermore, the coverage precentage of the capping agent plays |
992 |
> |
agent. Furthermore, the coverage percentage of the capping agent plays |
993 |
|
an important role in the interfacial thermal transport |
994 |
|
process. Moderately low coverages allow higher contact between capping |
995 |
|
agent and solvent, and thus could further enhance the heat transfer |
1026 |
|
Foundation under grant CHE-0848243. Computational time was provided by |
1027 |
|
the Center for Research Computing (CRC) at the University of Notre |
1028 |
|
Dame. |
1029 |
+ |
|
1030 |
+ |
\section{Supporting Information} |
1031 |
+ |
This information is available free of charge via the Internet at |
1032 |
+ |
http://pubs.acs.org. |
1033 |
+ |
|
1034 |
|
\newpage |
1035 |
|
|
1036 |
|
\bibliography{interfacial} |