1 |
< |
\documentclass[journal = jctcce, manuscript = article]{achemso} |
1 |
> |
\documentclass[journal = jpccck, manuscript = article]{achemso} |
2 |
|
\setkeys{acs}{usetitle = true} |
3 |
|
|
4 |
|
\usepackage{caption} |
25 |
|
\author{Kelsey M. Stocker} |
26 |
|
\author{J. Daniel Gezelter} |
27 |
|
\email{gezelter@nd.edu} |
28 |
< |
\affiliation[University of Notre Dame]{251 Nieuwland Science Hall\\ Department of Chemistry and Biochemistry\\ University of Notre Dame\\ Notre Dame, Indiana 46556} |
28 |
> |
\affiliation[University of Notre Dame]{251 Nieuwland Science Hall\\ |
29 |
> |
Department of Chemistry and Biochemistry\\ |
30 |
> |
University of Notre Dame\\ |
31 |
> |
Notre Dame, Indiana 46556} |
32 |
|
|
33 |
+ |
|
34 |
+ |
\keywords{Nanoparticles, interfaces, thermal conductance} |
35 |
+ |
|
36 |
|
\begin{document} |
37 |
|
|
38 |
|
\begin{tocentry} |
42 |
|
\newcolumntype{A}{p{1.5in}} |
43 |
|
\newcolumntype{B}{p{0.75in}} |
44 |
|
|
39 |
– |
% \author{Kelsey M. Stocker and J. Daniel |
40 |
– |
% Gezelter\footnote{Corresponding author. \ Electronic mail: |
41 |
– |
% gezelter@nd.edu} \\ |
42 |
– |
% 251 Nieuwland Science Hall, \\ |
43 |
– |
% Department of Chemistry and Biochemistry,\\ |
44 |
– |
% University of Notre Dame\\ |
45 |
– |
% Notre Dame, Indiana 46556} |
45 |
|
|
47 |
– |
%\date{\today} |
48 |
– |
|
49 |
– |
%\maketitle |
50 |
– |
|
51 |
– |
%\begin{doublespace} |
52 |
– |
|
46 |
|
\begin{abstract} |
47 |
|
|
48 |
|
\end{abstract} |
54 |
|
%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%% |
55 |
|
\section{Introduction} |
56 |
|
|
57 |
+ |
The thermal properties of various nanostructured interfaces have been |
58 |
+ |
the subject of intense experimental |
59 |
+ |
interest.\cite{Wilson:2002uq,PhysRevB.67.054302,doi:10.1021/jp048375k,PhysRevLett.96.186101,Wang10082007,doi:10.1021/jp8051888,PhysRevB.80.195406,doi:10.1021/la904855s} |
60 |
+ |
The interfacial thermal conductance ($G$) is the principal quantity of |
61 |
+ |
interest for understanding interfacial heat |
62 |
+ |
transport.\cite{cahill:793} Nanoparticles have a significant fraction |
63 |
+ |
of their atoms at interfaces, and the chemical details of these |
64 |
+ |
interfaces govern the thermal transport properties. |
65 |
+ |
|
66 |
+ |
Previously, reverse non-equilibrium molecular dynamics (RNEMD) methods |
67 |
+ |
have been applied to calculate the interfacial thermal conductance at |
68 |
+ |
metal / organic solvent interfaces that had been chemically protected |
69 |
+ |
by mixed-chain alkanethiolate groups.\cite{kuang:AuThl} These |
70 |
+ |
simulations suggest an explanation for the very large thermal |
71 |
+ |
conductivity at alkanethiol-capped metal surfaces. Specifically, the |
72 |
+ |
chemical bond between the metal and the ligand introduces a |
73 |
+ |
vibrational overlap that is not present without the protecting group, |
74 |
+ |
and the overlap between the vibrational spectra (metal to ligand, |
75 |
+ |
ligand to solvent) provides a mechanism for rapid thermal transport |
76 |
+ |
across the interface. The simulations also suggest that this |
77 |
+ |
phenomenon is a non-monotonic function of the fractional coverage of |
78 |
+ |
the surface, as moderate coverages allow diffusive heat transport of |
79 |
+ |
solvent molecules that have been in close contact with the ligands. |
80 |
+ |
|
81 |
+ |
Additionally, simulations of {\it mixed-chain} alkylthiolate surfaces |
82 |
+ |
showed that entrapped solvent can be very efficient at moving thermal |
83 |
+ |
energy away from the surface.\cite{Stocker2013} Trapped solvent that |
84 |
+ |
is orientationally coupled to the ordered ligands (and is less able to |
85 |
+ |
diffuse into the bulk) were able to double the thermal conductance of |
86 |
+ |
the interface. |
87 |
+ |
|
88 |
+ |
Recently, we extended RNEMD methods for use in non-periodic geometries |
89 |
+ |
by creating scaling/shearing moves between concentric regions of the |
90 |
+ |
simulation.\cite{Stocker:2014qq} The primary reason for developing a |
91 |
+ |
non-periodic variant of RNEMD is to investigate the role that {\it |
92 |
+ |
curved} nanoparticle surfaces play in heat and mass transport. On |
93 |
+ |
planar surfaces, we discovered that orientational ordering of surface |
94 |
+ |
protecting ligands had a large effect on the heat conduction from the |
95 |
+ |
metal to the solvent. Smaller nanoparticles have high surface |
96 |
+ |
curvature that creates gaps in well-ordered self-assembled monolayers, |
97 |
+ |
and the effect those gaps will have on the thermal conductance are |
98 |
+ |
unknown. |
99 |
+ |
|
100 |
+ |
|
101 |
+ |
|
102 |
|
%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%% |
103 |
|
% INTERFACIAL THERMAL CONDUCTANCE OF METALLIC NANOPARTICLES |
104 |
|
%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%% |
105 |
< |
\section{Interfacial Thermal Conductance of Metallic Nanoparticles} |
105 |
> |
%\section{Interfacial Thermal Conductance of Metallic Nanoparticles} |
106 |
|
|
107 |
< |
For a solvated nanoparticle, we can define a critical interfacial thermal conductance value, |
107 |
> |
For a solvated nanoparticle, we can define a critical value for the |
108 |
> |
interfacial thermal conductance, |
109 |
|
\begin{equation} |
110 |
< |
G_c = \frac{3 C_f \Lambda_f}{r C_p} |
110 |
> |
G_c = \frac{3 C_s \Lambda_s}{R C_p} |
111 |
|
\end{equation} |
112 |
+ |
which depends on the solvent heat capacity, $C_s$, solvent thermal |
113 |
+ |
conductivity, $\Lambda_s$, particle radius, $R$, and nanoparticle heat |
114 |
+ |
capacity, $C_p$.\cite{Wilson:2002uq} In the infinite interfacial |
115 |
+ |
thermal conductance limit $G >> G_c$, the particle cooling rate is |
116 |
+ |
limited by the solvent properties, $C_s$ and $\Lambda_s$. In the |
117 |
+ |
opposite limit ($G << G_c$), the heat dissipation is controlled by the |
118 |
+ |
thermal conductance of the particle / fluid interface. It is this |
119 |
+ |
regime with which we are concerned, where properties of the interface |
120 |
+ |
may be tuned to manipulate the rate of cooling for a solvated |
121 |
+ |
nanoparticle. Based on $G$ values from previous simulations of gold |
122 |
+ |
nanoparticles solvated in hexane and experimental results for solvated |
123 |
+ |
nanostructures, it appears that we are in the $G << G_c$ regime for |
124 |
+ |
gold nanoparticles of radius $< 400$ \AA\ solvated in hexane. The |
125 |
+ |
particles included in this study are more than an order of magnitude |
126 |
+ |
smaller than this critical radius. The heat dissipation should thus be |
127 |
+ |
controlled entirely by the surface features of the particle / ligand / |
128 |
+ |
solvent interface. |
129 |
|
|
74 |
– |
dependent upon the fluid heat capacity, $C_f$, fluid thermal conductivity, $\Lambda_f$, particle radius, $r$, and nanoparticle heat capacity, $C_p$.\cite{Wilson:2002uq} In the infinite interfacial thermal conductance limit $G >> G_c$, the particle cooling rate is limited by the fluid properties, $C_f$ and $\Lambda_f$. In the opposite limit ($G << G_c$), the heat dissipation is controlled by the thermal conductance of the particle / fluid interface. It is this regime with which we are concerned, where properties of the interface may be tuned to manipulate the rate of cooling for a solvated nanoparticle. Based on $G$ values from previous simulations of gold nanoparticles solvated in hexane and experimental results for solvated nanostructures, it appears that we are in the $G << G_c$ regime for gold nanoparticles of radius $<$ 400 \AA\ solvated in hexane. The particles included in this study are more than an order of magnitude smaller than this critical radius. The heat dissipation should thus be controlled entirely by the surface features of the particle / ligand / solvent interface. |
75 |
– |
|
130 |
|
% Understanding how the structural details of the interfaces affect the energy flow between the particle and its surroundings is essential in designing and functionalizing metallic nanoparticles for use in plasmonic photothermal therapies,\cite{Jain:2007ux,Petrova:2007ad,Gnyawali:2008lp,Mazzaglia:2008to,Huff:2007ye,Larson:2007hw} which rely on the ability of metallic nanoparticles to absorb light in the near-IR, a portion of the spectrum in which living tissue is very nearly transparent. The relevant physical property controlling the transfer of this energy as heat into the surrounding tissue is the interfacial thermal conductance, $G$, which can be somewhat difficult to determine experimentally.\cite{Wilson:2002uq,Plech:2005kx} |
131 |
|
% |
132 |
|
% Metallic particles have also been proposed for use in efficient thermal-transfer fluids, although careful experiments by Eapen \textit{et al.} have shown that metal-particle-based nanofluids have thermal conductivities that match Maxwell predictions.\cite{Eapen:2007th} The likely cause of previously reported non-Maxwell behavior\cite{Eastman:2001wb,Keblinski:2002bx,Lee:1999ct,Xue:2003ya,Xue:2004oa} is percolation networks of nanoparticles exchanging energy via the solvent,\cite{Eapen:2007mw} so it is important to get a detailed molecular picture of particle-ligand and ligand-solvent interactions in order to understand the thermal behavior of complex fluids. To date, there have been some reported values from experiment\cite{Wilson:2002uq,doi:10.1021jp8051888,doi:10.1021jp048375k,Ge2005,Park2012}) of $G$ for ligand-protected nanoparticles embedded in liquids, but there is still a significant gap in knowledge about how chemically distinct ligands or protecting groups will affect heat transport from the particles. In particular, the dearth of atomistic, dynamic information available from molecular dynamics simulations means that the heat transfer mechanisms at these nanoparticle surfaces remain largely unclear. |
136 |
|
%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%% |
137 |
|
\section{Structure of Self-Assembled Monolayers on Nanoparticles} |
138 |
|
|
139 |
< |
Though the ligand packing on planar surfaces is characterized for many different ligands and surface facets, it is not obvious \emph{a priori} how the same ligands will behave on the highly curved surfaces of nanoparticles. Thus, as more applications of ligand-stabilized nanostructures have become apparent, the structure and dynamics of ligands on metallic nanoparticles have been studied extensively.\cite{Badia1996:2,Badia1996,Henz2007,Badia1997:2,Badia1997,Badia2000} Badia, \textit{et al.} used transmission electron microscopy to determine that alkanethiol ligands on gold nanoparticles pack approximately 30\% more densely than on planar Au(111) surfaces.\cite{Badia1996:2} Subsequent experiments demonstrated that even at full coverages, surface curvature creates voids between linear ligand chains that can be filled via interdigitation of ligands on neighboring particles.\cite{Badia1996} The molecular dynamics simulations of Henz, \textit{et al.} indicate that at low coverages, the thiolate alkane chains will lie flat on the nanoparticle surface\cite{Henz2007} Above 90\% coverage, the ligands stand upright and recover the rigidity and tilt angle displayed on planar facets. Their simulations also indicate a high degree of mixing between the thiolate sulfur atoms and surface gold atoms at high coverages. |
139 |
> |
Though the ligand packing on planar surfaces is characterized for many |
140 |
> |
different ligands and surface facets, it is not obvious \emph{a |
141 |
> |
priori} how the same ligands will behave on the highly curved |
142 |
> |
surfaces of nanoparticles. Thus, as more applications of |
143 |
> |
ligand-stabilized nanostructures have become apparent, the structure |
144 |
> |
and dynamics of ligands on metallic nanoparticles have been studied |
145 |
> |
extensively.\cite{Badia1996:2,Badia1996,Henz2007,Badia1997:2,Badia1997,Badia2000} |
146 |
> |
Badia, \textit{et al.} used transmission electron microscopy to |
147 |
> |
determine that alkanethiol ligands on gold nanoparticles pack |
148 |
> |
approximately 30\% more densely than on planar Au(111) |
149 |
> |
surfaces.\cite{Badia1996:2} Subsequent experiments demonstrated that |
150 |
> |
even at full coverages, surface curvature creates voids between linear |
151 |
> |
ligand chains that can be filled via interdigitation of ligands on |
152 |
> |
neighboring particles.\cite{Badia1996} The molecular dynamics |
153 |
> |
simulations of Henz, \textit{et al.} indicate that at low coverages, |
154 |
> |
the thiolate alkane chains will lie flat on the nanoparticle |
155 |
> |
surface\cite{Henz2007} Above 90\% coverage, the ligands stand upright |
156 |
> |
and recover the rigidity and tilt angle displayed on planar |
157 |
> |
facets. Their simulations also indicate a high degree of mixing |
158 |
> |
between the thiolate sulfur atoms and surface gold atoms at high |
159 |
> |
coverages. |
160 |
|
|
161 |
|
%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%% |
162 |
|
% NON-PERIODIC VSS-RNEMD METHODOLOGY |
163 |
|
%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%% |
164 |
|
\section{Non-Periodic Velocity Shearing and Scaling RNEMD Methodology} |
165 |
|
|
166 |
< |
Non-periodic VSS-RNEMD, explained in detail in Chapter 4, periodically applies a series of velocity scaling and shearing moves at regular intervals to impose a flux between two concentric spherical regions. |
166 |
> |
Non-periodic VSS-RNEMD,\cite{Stocker:2014qq} periodically applies a |
167 |
> |
series of velocity scaling and shearing moves at regular intervals to |
168 |
> |
impose a flux between two concentric spherical regions. |
169 |
|
|
170 |
|
To simultaneously impose a thermal flux ($J_r$) between the shells we |
171 |
|
use energy conservation constraints, |
194 |
|
%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%% |
195 |
|
\subsection{Interfacial Thermal Conductance} |
196 |
|
|
197 |
< |
As described in Chapter 4, we can describe the thermal conductance of each spherical shell as the inverse Kapitza resistance. To describe the thermal conductance for an interface of considerable thickness, such as the ligand layers shown here, we can sum the individual thermal resistances of each concentric spherical shell to arrive at the total thermal resistance, or the inverse of the total interfacial thermal conductance: |
197 |
> |
We can describe the thermal conductance of each spherical shell as the |
198 |
> |
inverse Kapitza resistance. To describe the thermal conductance for an |
199 |
> |
interface of considerable thickness, such as the ligand layers shown |
200 |
> |
here, we can sum the individual thermal resistances of each concentric |
201 |
> |
spherical shell to arrive at the total thermal resistance, or the |
202 |
> |
inverse of the total interfacial thermal conductance: |
203 |
|
|
204 |
|
\begin{equation} |
205 |
|
\frac{1}{G} = R_\mathrm{total} = \frac{1}{q_r} \sum_i \left(T_{i+i} - |
336 |
|
%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%% |
337 |
|
\subsection{Mobility of Interfacial Solvent} |
338 |
|
|
339 |
< |
As in the planar case described in Chapter 3, I use a survival correlation function, $C(t)$, to measure the residence time of a solvent molecule in the nanoparticle thiolate layer. This function correlates the identity of all hexane molecules within the radial range of the thiolate layer at two separate times. If the solvent molecule is present at both times, the configuration contributes a $1$, while the absence of the molecule at the later time indicates that the solvent molecule has migrated into the bulk, and this configuration contributes a $0$. A steep decay in $C(t)$ indicates a high turnover rate of solvent molecules from the chain region to the bulk. We may define the escape rate for trapped solvent molecules at the interface as |
339 |
> |
We use a survival correlation function, $C(t)$, to measure the |
340 |
> |
residence time of a solvent molecule in the nanoparticle thiolate |
341 |
> |
layer.\cite{Stocker2013} This function correlates the identity of all |
342 |
> |
hexane molecules within the radial range of the thiolate layer at two |
343 |
> |
separate times. If the solvent molecule is present at both times, the |
344 |
> |
configuration contributes a $1$, while the absence of the molecule at |
345 |
> |
the later time indicates that the solvent molecule has migrated into |
346 |
> |
the bulk, and this configuration contributes a $0$. A steep decay in |
347 |
> |
$C(t)$ indicates a high turnover rate of solvent molecules from the |
348 |
> |
chain region to the bulk. We may define the escape rate for trapped |
349 |
> |
solvent molecules at the interface as |
350 |
|
|
351 |
|
\begin{equation} |
352 |
|
k_{escape} = \left( \int_0^T C(t) dt \right)^{-1} |
445 |
|
|
446 |
|
\bibliography{NPthiols} |
447 |
|
|
448 |
< |
\end{document} |
448 |
> |
\end{document} |