| 1 |
< |
\documentclass[11pt]{article} |
| 1 |
> |
\documentclass[journal = jpccck, manuscript = article]{achemso} |
| 2 |
> |
\setkeys{acs}{usetitle = true} |
| 3 |
> |
\usepackage{achemso} |
| 4 |
> |
\usepackage{caption} |
| 5 |
> |
\usepackage{float} |
| 6 |
> |
\usepackage{geometry} |
| 7 |
> |
\usepackage{natbib} |
| 8 |
> |
\usepackage{setspace} |
| 9 |
> |
\usepackage{xkeyval} |
| 10 |
> |
%%%%%%%%%%%%%%%%%%%%%%% |
| 11 |
|
\usepackage{amsmath} |
| 12 |
|
\usepackage{amssymb} |
| 13 |
|
\usepackage{times} |
| 15 |
|
\usepackage{setspace} |
| 16 |
|
\usepackage{endfloat} |
| 17 |
|
\usepackage{caption} |
| 18 |
< |
%\usepackage{tabularx} |
| 18 |
> |
\usepackage{tabularx} |
| 19 |
> |
\usepackage{longtable} |
| 20 |
|
\usepackage{graphicx} |
| 21 |
|
\usepackage{multirow} |
| 22 |
< |
%\usepackage{booktabs} |
| 23 |
< |
%\usepackage{bibentry} |
| 24 |
< |
%\usepackage{mathrsfs} |
| 25 |
< |
\usepackage[square, comma, sort&compress]{natbib} |
| 22 |
> |
\usepackage{multicol} |
| 23 |
> |
\mciteErrorOnUnknownfalse |
| 24 |
> |
%\usepackage{epstopdf} |
| 25 |
> |
|
| 26 |
> |
\usepackage[version=3]{mhchem} % this is a great package for formatting chemical reactions |
| 27 |
> |
% \usepackage[square, comma, sort&compress]{natbib} |
| 28 |
|
\usepackage{url} |
| 29 |
|
\pagestyle{plain} \pagenumbering{arabic} \oddsidemargin 0.0cm |
| 30 |
|
\evensidemargin 0.0cm \topmargin -21pt \headsep 10pt \textheight |
| 31 |
< |
9.0in \textwidth 6.5in \brokenpenalty=10000 |
| 31 |
> |
9.0in \textwidth 6.5in \brokenpenalty=1110000 |
| 32 |
|
|
| 33 |
|
% double space list of tables and figures |
| 34 |
|
%\AtBeginDelayedFloats{\renewcomand{\baselinestretch}{1.66}} |
| 35 |
|
\setlength{\abovecaptionskip}{20 pt} |
| 36 |
|
\setlength{\belowcaptionskip}{30 pt} |
| 37 |
+ |
% \bibpunct{}{}{,}{s}{}{;} |
| 38 |
|
|
| 39 |
< |
\bibpunct{}{}{,}{s}{}{;} |
| 40 |
< |
\bibliographystyle{achemso} |
| 39 |
> |
%\citestyle{nature} |
| 40 |
> |
% \bibliographystyle{achemso} |
| 41 |
|
|
| 42 |
< |
\begin{document} |
| 42 |
> |
\title{Molecular Dynamics simulations of the surface reconstructions |
| 43 |
> |
of Pt(557) and Au(557) under exposure to CO} |
| 44 |
|
|
| 45 |
+ |
\author{Joseph R. Michalka} |
| 46 |
+ |
\author{Patrick W. McIntyre} |
| 47 |
+ |
\author{J. Daniel Gezelter} |
| 48 |
+ |
\email{gezelter@nd.edu} |
| 49 |
+ |
\affiliation[University of Notre Dame]{251 Nieuwland Science Hall\\ |
| 50 |
+ |
Department of Chemistry and Biochemistry\\ University of Notre |
| 51 |
+ |
Dame\\ Notre Dame, Indiana 46556} |
| 52 |
|
|
| 53 |
+ |
\keywords{} |
| 54 |
+ |
|
| 55 |
+ |
\begin{document} |
| 56 |
+ |
|
| 57 |
+ |
|
| 58 |
|
%% |
| 59 |
|
%Introduction |
| 60 |
|
% Experimental observations |
| 73 |
|
%Summary |
| 74 |
|
%% |
| 75 |
|
|
| 50 |
– |
%Title |
| 51 |
– |
\title{Molecular Dynamics simulations of the surface reconstructions |
| 52 |
– |
of Pt(557) and Au(557) under exposure to CO} |
| 76 |
|
|
| 54 |
– |
\author{Joseph R. Michalka, Patrick W. McIntyre and J. Daniel |
| 55 |
– |
Gezelter\footnote{Corresponding author. \ Electronic mail: gezelter@nd.edu} \\ |
| 56 |
– |
Department of Chemistry and Biochemistry,\\ |
| 57 |
– |
University of Notre Dame\\ |
| 58 |
– |
Notre Dame, Indiana 46556} |
| 59 |
– |
|
| 60 |
– |
%Date |
| 61 |
– |
\date{Dec 15, 2012} |
| 62 |
– |
|
| 63 |
– |
%authors |
| 64 |
– |
|
| 65 |
– |
% make the title |
| 66 |
– |
\maketitle |
| 67 |
– |
|
| 68 |
– |
\begin{doublespace} |
| 69 |
– |
|
| 77 |
|
\begin{abstract} |
| 78 |
< |
We examine potential surface reconstructions of Pt and Au (557) under various CO coverages using molecular dynamics in order to find possible mechanisms and dynamics for the restructuring. The metal-CO interactions were parameterized as part of this work so that a large scale treatment of this system could be undertaken. The relative binding strengths of the metal-CO interactions were found to play a large role with regards to step edge stability and adatom diffusion. A small correlation between coverage and the size of the diffusion constant was also determined. These results appear sufficient to explain the reconstructions observed on the Pt systems and the lack of reconstructions on the Au systems. |
| 78 |
> |
The mechanism and dynamics of surface reconstructions of Pt(557) and |
| 79 |
> |
Au(557) exposed to various coverages of carbon monoxide (CO) were |
| 80 |
> |
investigated using molecular dynamics simulations. Metal-CO |
| 81 |
> |
interactions were parameterized from experimental data and |
| 82 |
> |
plane-wave Density Functional Theory (DFT) calculations. The large |
| 83 |
> |
difference in binding strengths of the Pt-CO and Au-CO interactions |
| 84 |
> |
was found to play a significant role in step-edge stability and |
| 85 |
> |
adatom diffusion constants. Various mechanisms for CO-mediated step |
| 86 |
> |
wandering and step doubling were investigated on the Pt(557) |
| 87 |
> |
surface. We find that the energetics of CO adsorbed to the surface |
| 88 |
> |
can explain the step-doubling reconstruction observed on Pt(557) and |
| 89 |
> |
the lack of such a reconstruction on the Au(557) surface. |
| 90 |
|
\end{abstract} |
| 91 |
|
|
| 92 |
|
\newpage |
| 118 |
|
reversible restructuring under exposure to moderate pressures of |
| 119 |
|
carbon monoxide.\cite{Tao:2010} |
| 120 |
|
|
| 121 |
< |
This work is an attempt to understand the mechanism and timescale for |
| 121 |
> |
This work is an investigation into the mechanism and timescale for the Pt(557) \& Au(557) |
| 122 |
|
surface restructuring using molecular simulations. Since the dynamics |
| 123 |
|
of the process are of particular interest, we employ classical force |
| 124 |
|
fields that represent a compromise between chemical accuracy and the |
| 125 |
|
computational efficiency necessary to simulate the process of interest. |
| 126 |
< |
|
| 127 |
< |
Restructuring can occur as a result of specific interactions of the |
| 110 |
< |
catalyst with adsorbates. In this work, two metal systems exposed |
| 126 |
> |
Since restructuring typically occurs as a result of specific interactions of the |
| 127 |
> |
catalyst with adsorbates, in this work, two metal systems exposed |
| 128 |
|
to carbon monoxide were examined. The Pt(557) surface has already been shown |
| 129 |
< |
to reconstruct under certain conditions. The Au(557) surface, because |
| 130 |
< |
of a weaker interaction with CO, is less likely to undergo this kind |
| 131 |
< |
of reconstruction. MORE HERE ON PT AND AU PREVIOUS WORK. |
| 129 |
> |
to undergo a large scale reconstruction under certain conditions.\cite{Tao:2010} |
| 130 |
> |
The Au(557) surface, because of a weaker interaction with CO, is less |
| 131 |
> |
likely to undergo this kind of reconstruction. However, Peters {\it et al}.\cite{Peters:2000} |
| 132 |
> |
and Piccolo {\it et al}.\cite{Piccolo:2004} have both observed CO-induced |
| 133 |
> |
reconstruction of a Au(111) surface. Peters {\it et al}. saw a relaxation to the |
| 134 |
> |
22 x $\sqrt{3}$ cell. They argued that only a few Au atoms |
| 135 |
> |
become adatoms, limiting the stress of this reconstruction, while |
| 136 |
> |
allowing the rest to relax and approach the ideal (111) |
| 137 |
> |
configuration. They did not see the usual herringbone pattern on Au(111) being greatly |
| 138 |
> |
affected by this relaxation. Piccolo {\it et al}. on the other hand, did see a |
| 139 |
> |
disruption of the herringbone pattern as CO was adsorbed to the |
| 140 |
> |
surface. Both groups suggested that the preference CO shows for |
| 141 |
> |
low-coordinated Au atoms was the primary driving force for the reconstruction. |
| 142 |
|
|
| 143 |
+ |
|
| 144 |
+ |
|
| 145 |
|
%Platinum molecular dynamics |
| 146 |
|
%gold molecular dynamics |
| 147 |
|
|
| 148 |
|
\section{Simulation Methods} |
| 149 |
< |
The challenge in modeling any solid/gas interface problem is the |
| 149 |
> |
The challenge in modeling any solid/gas interface is the |
| 150 |
|
development of a sufficiently general yet computationally tractable |
| 151 |
|
model of the chemical interactions between the surface atoms and |
| 152 |
|
adsorbates. Since the interfaces involved are quite large (10$^3$ - |
| 153 |
< |
10$^6$ atoms) and respond slowly to perturbations, {\it ab initio} |
| 153 |
> |
10$^4$ atoms) and respond slowly to perturbations, {\it ab initio} |
| 154 |
|
molecular dynamics |
| 155 |
|
(AIMD),\cite{KRESSE:1993ve,KRESSE:1993qf,KRESSE:1994ul} Car-Parrinello |
| 156 |
|
methods,\cite{CAR:1985bh,Izvekov:2000fv,Guidelli:2000fy} and quantum |
| 162 |
|
Coulomb potential. For this work, we have used classical molecular |
| 163 |
|
dynamics with potential energy surfaces that are specifically tuned |
| 164 |
|
for transition metals. In particular, we used the EAM potential for |
| 165 |
< |
Au-Au and Pt-Pt interactions\cite{EAM}, while modeling the CO using a rigid |
| 165 |
> |
Au-Au and Pt-Pt interactions.\cite{Foiles86} The CO was modeled using a rigid |
| 166 |
|
three-site model developed by Straub and Karplus for studying |
| 167 |
|
photodissociation of CO from myoglobin.\cite{Straub} The Au-CO and |
| 168 |
|
Pt-CO cross interactions were parameterized as part of this work. |
| 175 |
|
methods,\cite{Daw84,Foiles86,Johnson89,Daw89,Plimpton93,Voter95a,Lu97,Alemany98} |
| 176 |
|
but other models like the Finnis-Sinclair\cite{Finnis84,Chen90} and |
| 177 |
|
the quantum-corrected Sutton-Chen method\cite{QSC,Qi99} have simpler |
| 178 |
< |
parameter sets. The glue model of Ercolessi {\it et al.} is among the |
| 179 |
< |
fastest of these density functional approaches.\cite{Ercolessi88} In |
| 180 |
< |
all of these models, atoms are conceptualized as a positively charged |
| 178 |
> |
parameter sets. The glue model of Ercolessi {\it et al}.\cite{Ercolessi88} is among the |
| 179 |
> |
fastest of these density functional approaches. In |
| 180 |
> |
all of these models, atoms are treated as a positively charged |
| 181 |
|
core with a radially-decaying valence electron distribution. To |
| 182 |
|
calculate the energy for embedding the core at a particular location, |
| 183 |
|
the electron density due to the valence electrons at all of the other |
| 212 |
|
melting,\cite{Belonoshko00,sankaranarayanan:155441,Sankaranarayanan:2005lr} |
| 213 |
|
fracture,\cite{Shastry:1996qg,Shastry:1998dx} crack |
| 214 |
|
propagation,\cite{BECQUART:1993rg} and alloying |
| 215 |
< |
dynamics.\cite{Shibata:2002hh} All of these potentials have their |
| 216 |
< |
strengths and weaknesses. One of the strengths common to all of the |
| 217 |
< |
methods is the relatively large library of metals for which these |
| 218 |
< |
potentials have been |
| 219 |
< |
parameterized.\cite{Foiles86,PhysRevB.37.3924,Rifkin1992,mishin99:_inter,mishin01:cu,mishin02:b2nial,zope03:tial_ap,mishin05:phase_fe_ni} |
| 215 |
> |
dynamics.\cite{Shibata:2002hh} One of EAM's strengths |
| 216 |
> |
is its sensitivity to small changes in structure. This arises |
| 217 |
> |
because interactions |
| 218 |
> |
up to the third nearest neighbor were taken into account in the parameterization.\cite{Voter95a} |
| 219 |
> |
Comparing that to the glue model of Ercolessi {\it et al}.\cite{Ercolessi88} |
| 220 |
> |
which is only parameterized up to the nearest-neighbor |
| 221 |
> |
interactions, EAM is a suitable choice for systems where |
| 222 |
> |
the bulk properties are of secondary importance to low-index |
| 223 |
> |
surface structures. Additionally, the similarity of EAM's functional |
| 224 |
> |
treatment of the embedding energy to standard density functional |
| 225 |
> |
theory (DFT) makes fitting DFT-derived cross potentials with adsorbates somewhat easier. |
| 226 |
> |
\cite{Foiles86,PhysRevB.37.3924,Rifkin1992,mishin99:_inter,mishin01:cu,mishin02:b2nial,zope03:tial_ap,mishin05:phase_fe_ni} |
| 227 |
|
|
| 228 |
+ |
|
| 229 |
+ |
|
| 230 |
+ |
|
| 231 |
|
\subsection{Carbon Monoxide model} |
| 232 |
|
Previous explanations for the surface rearrangements center on |
| 233 |
< |
the large linear quadrupole moment of carbon monoxide. |
| 233 |
> |
the large linear quadrupole moment of carbon monoxide.\cite{Tao:2010} |
| 234 |
|
We used a model first proposed by Karplus and Straub to study |
| 235 |
|
the photodissociation of CO from myoglobin because it reproduces |
| 236 |
|
the quadrupole moment well.\cite{Straub} The Straub and |
| 237 |
< |
Karplus model, treats CO as a rigid three site molecule which places a massless M |
| 238 |
< |
site at the center of mass position along the CO bond. The geometry used along |
| 239 |
< |
with the interaction parameters are reproduced in Table~\ref{tab:CO}. The effective |
| 237 |
> |
Karplus model treats CO as a rigid three site molecule with a massless M |
| 238 |
> |
site at the molecular center of mass. The geometry and interaction |
| 239 |
> |
parameters are reproduced in Table~\ref{tab:CO}. The effective |
| 240 |
|
dipole moment, calculated from the assigned charges, is still |
| 241 |
|
small (0.35 D) while the linear quadrupole (-2.40 D~\AA) is close |
| 242 |
|
to the experimental (-2.63 D~\AA)\cite{QuadrupoleCO} and quantum |
| 245 |
|
\begin{table}[H] |
| 246 |
|
\caption{Positions, Lennard-Jones parameters ($\sigma$ and |
| 247 |
|
$\epsilon$), and charges for the CO-CO |
| 248 |
< |
interactions borrowed from Ref. \bibpunct{}{}{,}{n}{}{,} \protect\cite{Straub}. Distances are in \AA~, energies are |
| 248 |
> |
interactions in Ref.\bibpunct{}{}{,}{n}{}{,} \protect\cite{Straub}. Distances are in \AA, energies are |
| 249 |
|
in kcal/mol, and charges are in atomic units.} |
| 250 |
|
\centering |
| 251 |
|
\begin{tabular}{| c | c | ccc |} |
| 252 |
|
\hline |
| 253 |
|
& {\it z} & $\sigma$ & $\epsilon$ & q\\ |
| 254 |
|
\hline |
| 255 |
< |
\textbf{C} & -0.6457 & 0.0262 & 3.83 & -0.75 \\ |
| 256 |
< |
\textbf{O} & 0.4843 & 0.1591 & 3.12 & -0.85 \\ |
| 255 |
> |
\textbf{C} & -0.6457 & 3.83 & 0.0262 & -0.75 \\ |
| 256 |
> |
\textbf{O} & 0.4843 & 3.12 & 0.1591 & -0.85 \\ |
| 257 |
|
\textbf{M} & 0.0 & - & - & 1.6 \\ |
| 258 |
|
\hline |
| 259 |
|
\end{tabular} |
| 262 |
|
|
| 263 |
|
\subsection{Cross-Interactions between the metals and carbon monoxide} |
| 264 |
|
|
| 265 |
< |
Since the adsorption of CO onto a platinum surface has been the focus |
| 265 |
> |
Since the adsorption of CO onto a Pt surface has been the focus |
| 266 |
|
of much experimental \cite{Yeo, Hopster:1978, Ertl:1977, Kelemen:1979} |
| 267 |
|
and theoretical work |
| 268 |
|
\cite{Beurden:2002ys,Pons:1986,Deshlahra:2009,Feibelman:2001,Mason:2004} |
| 269 |
|
there is a significant amount of data on adsorption energies for CO on |
| 270 |
< |
clean metal surfaces. Parameters reported by Korzeniewski {\it et |
| 271 |
< |
al.}\cite{Pons:1986} were a starting point for our fits, which were |
| 270 |
> |
clean metal surfaces. An earlier model by Korzeniewski {\it et |
| 271 |
> |
al.}\cite{Pons:1986} served as a starting point for our fits. The parameters were |
| 272 |
|
modified to ensure that the Pt-CO interaction favored the atop binding |
| 273 |
< |
position on Pt(111). These parameters are reproduced in Table~\ref{tab:co_parameters} |
| 274 |
< |
This resulted in binding energies that are slightly higher |
| 273 |
> |
position on Pt(111). These parameters are reproduced in Table~\ref{tab:co_parameters}. |
| 274 |
> |
The modified parameters yield binding energies that are slightly higher |
| 275 |
|
than the experimentally-reported values as shown in Table~\ref{tab:co_energies}. Following Korzeniewski |
| 276 |
< |
{\it et al.},\cite{Pons:1986} the Pt-C interaction was fit to a deep |
| 277 |
< |
Lennard-Jones interaction to mimic strong, but short-ranged partial |
| 276 |
> |
{\it et al}.,\cite{Pons:1986} the Pt-C interaction was fit to a deep |
| 277 |
> |
Lennard-Jones interaction to mimic strong, but short-ranged, partial |
| 278 |
|
binding between the Pt $d$ orbitals and the $\pi^*$ orbital on CO. The |
| 279 |
< |
Pt-O interaction was parameterized to a Morse potential at a larger |
| 280 |
< |
minimum distance, ($r_o$). This was chosen so that the C would be preferred |
| 281 |
< |
over O as the binder to the surface. In most cases, this parameterization contributes a weak |
| 279 |
> |
Pt-O interaction was modeled with a Morse potential with a large |
| 280 |
> |
equilibrium distance, ($r_o$). These choices ensure that the C is preferred |
| 281 |
> |
over O as the surface-binding atom. In most geometries, the Pt-O parameterization contributes a weak |
| 282 |
|
repulsion which favors the atop site. The resulting potential-energy |
| 283 |
|
surface suitably recovers the calculated Pt-C separation length |
| 284 |
|
(1.6~\AA)\cite{Beurden:2002ys} and affinity for the atop binding |
| 289 |
|
%same cutoff for slab and slab + CO ? seems low, although feibelmen had values around there... |
| 290 |
|
The Au-C and Au-O cross-interactions were also fit using Lennard-Jones and |
| 291 |
|
Morse potentials, respectively, to reproduce Au-CO binding energies. |
| 292 |
< |
The limited experimental data for CO adsorption on Au lead us to refine our fits against DFT. |
| 292 |
> |
The limited experimental data for CO adsorption on Au required refining the fits against plane-wave DFT calculations. |
| 293 |
|
Adsorption energies were obtained from gas-surface DFT calculations with a |
| 294 |
|
periodic supercell plane-wave basis approach, as implemented in the |
| 295 |
< |
{\sc Quantum ESPRESSO} package.\cite{QE-2009} Electron cores are |
| 295 |
> |
{\sc Quantum ESPRESSO} package.\cite{QE-2009} Electron cores were |
| 296 |
|
described with the projector augmented-wave (PAW) |
| 297 |
|
method,\cite{PhysRevB.50.17953,PhysRevB.59.1758} with plane waves |
| 298 |
|
included to an energy cutoff of 20 Ry. Electronic energies are |
| 306 |
|
performed until the energy difference between subsequent steps |
| 307 |
|
was less than $10^{-8}$ Ry. Nonspin-polarized supercell calculations |
| 308 |
|
were performed with a 4~x~4~x~4 Monkhorst-Pack {\bf k}-point sampling of the first Brillouin |
| 309 |
< |
zone.\cite{Monkhorst:1976,PhysRevB.13.5188} The relaxed gold slab was |
| 309 |
> |
zone.\cite{Monkhorst:1976} The relaxed gold slab was |
| 310 |
|
then used in numerous single point calculations with CO at various |
| 311 |
|
heights (and angles relative to the surface) to allow fitting of the |
| 312 |
|
empirical force field. |
| 313 |
|
|
| 314 |
|
%Hint at future work |
| 315 |
|
The parameters employed for the metal-CO cross-interactions in this work |
| 316 |
< |
are shown in Table~\ref{co_parameters} and the binding energies on the |
| 317 |
< |
(111) surfaces are displayed in Table~\ref{co_energies}. Charge transfer |
| 318 |
< |
and polarization are neglected in this model, although these effects are likely to |
| 319 |
< |
affect binding energies and binding site preferences, and will be added in |
| 281 |
< |
a future work.\cite{Deshlahra:2012,StreitzMintmire} |
| 316 |
> |
are shown in Table~\ref{tab:co_parameters} and the binding energies on the |
| 317 |
> |
(111) surfaces are displayed in Table~\ref{tab:co_energies}. Charge transfer |
| 318 |
> |
and polarization are neglected in this model, although these effects could have |
| 319 |
> |
an effect on binding energies and binding site preferences. |
| 320 |
|
|
| 321 |
|
%Table of Parameters |
| 322 |
|
%Pt Parameter Set 9 |
| 323 |
|
%Au Parameter Set 35 |
| 324 |
|
\begin{table}[H] |
| 325 |
< |
\caption{Best fit parameters for metal-CO cross-interactions. Metal-C |
| 326 |
< |
interactions are modeled with Lennard-Jones potential, while the |
| 327 |
< |
(mostly-repulsive) metal-O interactions were fit to Morse |
| 325 |
> |
\caption{Best fit parameters for metal-CO cross-interactions. Metal-C |
| 326 |
> |
interactions are modeled with Lennard-Jones potentials. While the |
| 327 |
> |
metal-O interactions were fit to Morse |
| 328 |
|
potentials. Distances are given in \AA~and energies in kcal/mol. } |
| 329 |
|
\centering |
| 330 |
|
\begin{tabular}{| c | cc | c | ccc |} |
| 341 |
|
|
| 342 |
|
%Table of energies |
| 343 |
|
\begin{table}[H] |
| 344 |
< |
\caption{Adsorption energies for CO on M(111) using the potentials |
| 345 |
< |
described in this work. All values are in eV} |
| 344 |
> |
\caption{Adsorption energies for a single CO at the atop site on M(111) at the atop site using the potentials |
| 345 |
> |
described in this work. All values are in eV.} |
| 346 |
|
\centering |
| 347 |
|
\begin{tabular}{| c | cc |} |
| 348 |
|
\hline |
| 351 |
|
\multirow{2}{*}{\textbf{Pt-CO}} & \multirow{2}{*}{-1.9} & -1.4 \bibpunct{}{}{,}{n}{}{,} |
| 352 |
|
(Ref. \protect\cite{Kelemen:1979}) \\ |
| 353 |
|
& & -1.9 \bibpunct{}{}{,}{n}{}{,} (Ref. \protect\cite{Yeo}) \\ \hline |
| 354 |
< |
\textbf{Au-CO} & -0.39 & -0.40 \bibpunct{}{}{,}{n}{}{,} (Ref. \protect\cite{TPD_Gold}) \\ |
| 354 |
> |
\textbf{Au-CO} & -0.39 & -0.40 \bibpunct{}{}{,}{n}{}{,} (Ref. \protect\cite{TPDGold}) \\ |
| 355 |
|
\hline |
| 356 |
|
\end{tabular} |
| 357 |
|
\label{tab:co_energies} |
| 358 |
|
\end{table} |
| 359 |
|
|
| 360 |
|
\subsection{Pt(557) and Au(557) metal interfaces} |
| 361 |
< |
|
| 362 |
< |
Our model systems are composed of 3888 Pt atoms and 3384 Au atoms in a |
| 363 |
< |
FCC crystal that have been cut along the 557 plane so that they are |
| 364 |
< |
periodic in the {\it x} and {\it y} directions, and have been rotated |
| 365 |
< |
to expose two parallel 557 cuts along the positive and negative {\it |
| 366 |
< |
z}-axis. Simulations of the bare metal interfaces at temperatures |
| 367 |
< |
ranging from 300~K to 1200~K were done to observe the relative |
| 361 |
> |
Our Pt system is an orthorhombic periodic box of dimensions |
| 362 |
> |
54.482~x~50.046~x~120.88~\AA~while our Au system has |
| 363 |
> |
dimensions of 57.4~x~51.9285~x~100~\AA. The metal slabs |
| 364 |
> |
are 9 and 8 atoms deep respectively, corresponding to a slab |
| 365 |
> |
thickness of $\sim$21~\AA~ for Pt and $\sim$19~\AA~for Au. |
| 366 |
> |
The systems are arranged in a FCC crystal that have been cut |
| 367 |
> |
along the (557) plane so that they are periodic in the {\it x} and |
| 368 |
> |
{\it y} directions, and have been oriented to expose two aligned |
| 369 |
> |
(557) cuts along the extended {\it z}-axis. Simulations of the |
| 370 |
> |
bare metal interfaces at temperatures ranging from 300~K to |
| 371 |
> |
1200~K were performed to confirm the relative |
| 372 |
|
stability of the surfaces without a CO overlayer. |
| 373 |
|
|
| 374 |
< |
The different bulk (and surface) melting temperatures (1337~K for Au |
| 375 |
< |
and 2045~K for Pt) suggest that the reconstruction may happen at |
| 376 |
< |
different temperatures for the two metals. To copy experimental |
| 335 |
< |
conditions for the CO-exposed surfaces, the bare surfaces were |
| 374 |
> |
The different bulk melting temperatures predicted by EAM (1345~$\pm$~10~K for Au\cite{Au:melting} |
| 375 |
> |
and $\sim$~2045~K for Pt\cite{Pt:melting}) suggest that any possible reconstruction should happen at |
| 376 |
> |
different temperatures for the two metals. The bare Au and Pt surfaces were |
| 377 |
|
initially run in the canonical (NVT) ensemble at 800~K and 1000~K |
| 378 |
< |
respectively for 100 ps. Each surface was exposed to a range of CO |
| 378 |
> |
respectively for 100 ps. The two surfaces were relatively stable at these |
| 379 |
> |
temperatures when no CO was present, but experienced increased surface |
| 380 |
> |
mobility on addition of CO. Each surface was then dosed with different concentrations of CO |
| 381 |
|
that was initially placed in the vacuum region. Upon full adsorption, |
| 382 |
< |
these amounts correspond to 0\%, 5\%, 25\%, 33\%, and 50\% surface |
| 383 |
< |
coverage. Because of the difference in binding energies, the platinum |
| 384 |
< |
systems very rarely had CO that was not bound to the surface, while |
| 385 |
< |
the gold surfaces often had a significant CO population in the gas |
| 382 |
> |
these concentrations correspond to 0\%, 5\%, 25\%, 33\%, and 50\% surface |
| 383 |
> |
coverage. Higher coverages resulted in the formation of a double layer of CO, |
| 384 |
> |
which introduces artifacts that are not relevant to (557) reconstruction. |
| 385 |
> |
Because of the difference in binding energies, nearly all of the CO was bound to the Pt surface, while |
| 386 |
> |
the Au surfaces often had a significant CO population in the gas |
| 387 |
|
phase. These systems were allowed to reach thermal equilibrium (over |
| 388 |
< |
5 ns) before being shifted to the microcanonical (NVE) ensemble for |
| 389 |
< |
data collection. All of the systems examined had at least 40 ns in the |
| 390 |
< |
data collection stage, although simulation times for some of the |
| 391 |
< |
systems exceeded 200ns. All simulations were run using the open |
| 392 |
< |
source molecular dynamics package, OpenMD.\cite{Ewald,OOPSE,OpenMD} |
| 388 |
> |
5~ns) before being run in the microcanonical (NVE) ensemble for |
| 389 |
> |
data collection. All of the systems examined had at least 40~ns in the |
| 390 |
> |
data collection stage, although simulation times for some Pt of the |
| 391 |
> |
systems exceeded 200~ns. Simulations were carried out using the open |
| 392 |
> |
source molecular dynamics package, OpenMD.\cite{Ewald,OOPSE,openmd} |
| 393 |
|
|
| 394 |
< |
% Just results, leave discussion for discussion section |
| 395 |
< |
% structure |
| 396 |
< |
% Pt: step wandering, double layers, no triangular motifs |
| 397 |
< |
% Au: step wandering, no double layers |
| 398 |
< |
% dynamics |
| 355 |
< |
% diffusion |
| 356 |
< |
% time scale, formation, breakage |
| 394 |
> |
|
| 395 |
> |
|
| 396 |
> |
|
| 397 |
> |
% RESULTS |
| 398 |
> |
% |
| 399 |
|
\section{Results} |
| 400 |
|
\subsection{Structural remodeling} |
| 401 |
< |
Tao {\it et al.} showed experimentally that the Pt(557) surface undergoes |
| 402 |
< |
two separate reconstructions upon CO adsorption.\cite{Tao:2010} The first |
| 403 |
< |
reconstruction involves a doubling of the step height and plateau length. Similar |
| 404 |
< |
behavior has been seen to occur on numerous surfaces at varying conditions.\cite{Williams:1994,Williams:1991,Pearl} |
| 405 |
< |
Of the two systems we examined, the Platinum system showed the most surface |
| 406 |
< |
reconstruction. Additionally, the amount of reconstruction appears to be |
| 407 |
< |
dependent on the amount of CO adsorbed upon the surface. This result is likely |
| 408 |
< |
related to the effect that coverage has on surface diffusion. While both systems |
| 409 |
< |
displayed step edge wandering, only the Pt surface underwent doubling within |
| 410 |
< |
the time scales we were modeling. Specifically only the 50 \% coverage Pt system |
| 411 |
< |
was observed to undergo a complete doubling in the time scales we were able to monitor. |
| 370 |
< |
This event encouraged us to allow that specific system to run continuously during which two |
| 371 |
< |
more double layers were created. The other systems, not displaying any large scale changes |
| 372 |
< |
of interest, were all stopped after 40 ns of simulation. Neverthless, the other Platinum systems tended to show |
| 373 |
< |
more cumulative lateral movement of the step edges when compared to the Gold systems. |
| 374 |
< |
The 50 \% Pt system is highlighted in figure \ref{fig:reconstruct} at various times along the |
| 375 |
< |
simulation showing the evolution of the system. |
| 401 |
> |
The bare metal surfaces experienced minor roughening of the |
| 402 |
> |
step-edge because of the elevated temperatures, but the (557) |
| 403 |
> |
face was stable throughout the simulations. The surface of both |
| 404 |
> |
systems, upon dosage of CO, began to undergo extensive remodeling |
| 405 |
> |
that was not observed in the bare systems. Reconstructions of |
| 406 |
> |
the Au systems were limited to breakup of the step-edges and |
| 407 |
> |
some step wandering. The lower coverage Pt systems experienced |
| 408 |
> |
similar restructuring but to a greater extent. The 50\% coverage |
| 409 |
> |
Pt system was unique among our simulations in that it formed |
| 410 |
> |
well-defined and stable double layers through step coalescence, |
| 411 |
> |
similar to results reported by Tao {\it et al}.\cite{Tao:2010} |
| 412 |
|
|
| 377 |
– |
The second reconstruction on the Pt(557) surface observed by Tao involved the |
| 378 |
– |
formation of triangular clusters that stretched across the plateau between two step edges. |
| 379 |
– |
Neither system, within our simulated time scales, experiences this reconstruction. A constructed |
| 380 |
– |
system in which the triangular motifs were constructed on the surface will be explored in future |
| 381 |
– |
work and is shown in the supporting information. |
| 413 |
|
|
| 414 |
< |
\subsection{Dynamics} |
| 415 |
< |
While atomistic-like simulations of stepped surfaces have been performed before \cite{}, they tend to be |
| 416 |
< |
performed using Monte Carlo techniques\cite{Williams:1991,Williams:1994}. This allows them to efficiently sample the thermodynamic |
| 417 |
< |
landscape but at the expense of ignoring the dynamics of the system. Previous work, using STM \cite{Pearl}, |
| 418 |
< |
has been able to visualize the coalescing of steps of (system). The time scale of the image acquisition, ~ 70 s/image |
| 419 |
< |
provides an upper bounds for the time required for the doubling to actually occur. While statistical treatments |
| 420 |
< |
of step edges are adept at analyzing such systems, it is important to remember that the edges are made |
| 421 |
< |
up of individual atoms and thus can be examined in numerous ways. |
| 414 |
> |
\subsubsection{Step wandering} |
| 415 |
> |
The 0\% coverage surfaces for both metals showed minimal |
| 416 |
> |
step-wandering at their respective temperatures. As the CO |
| 417 |
> |
coverage increased however, the mobility of the surface atoms, |
| 418 |
> |
described through adatom diffusion and step-edge wandering, |
| 419 |
> |
also increased. Except for the 50\% Pt system where step |
| 420 |
> |
coalescence occurred, the step-edges in the other simulations |
| 421 |
> |
preferred to keep nearly the same distance between steps as in |
| 422 |
> |
the original (557) lattice, $\sim$13\AA~for Pt and $\sim$14\AA~for Au. |
| 423 |
> |
Previous work by Williams {\it et al}.\cite{Williams:1991, Williams:1994} |
| 424 |
> |
highlights the repulsion that exists between step-edges even |
| 425 |
> |
when no direct interactions are present in the system. This |
| 426 |
> |
repulsion is caused by an entropic barrier that arises from |
| 427 |
> |
the fact that steps cannot cross over one another. This entropic |
| 428 |
> |
repulsion does not completely define the interactions between |
| 429 |
> |
steps, however, so it is possible to observe step coalescence |
| 430 |
> |
on some surfaces.\cite{Williams:1991} The presence and |
| 431 |
> |
concentration of adsorbates, as shown in this work, can |
| 432 |
> |
affect step-step interactions, potentially leading to a new |
| 433 |
> |
surface structure as the thermodynamic equilibrium. |
| 434 |
|
|
| 435 |
< |
\subsubsection{Transport of surface metal atoms} |
| 436 |
< |
%forcedSystems/stepSeparation |
| 437 |
< |
The movement of a step edge is a cooperative effect arising from the individual movements of the atoms |
| 438 |
< |
making up the step. An ideal metal surface displaying a low index facet (111, 100, 110) is unlikely to |
| 439 |
< |
experience much surface diffusion because of the large energetic barrier to lift an atom out of the surface. |
| 440 |
< |
For our surfaces however, the presence of step edges provide a source for mobile metal atoms. Breaking away |
| 441 |
< |
from the step edge still imposes an energetic penalty around 40 kcal/mole, but is much less than lifting the same metal |
| 442 |
< |
atom out from the surface, > 60 kcal/mole, and the penalty lowers even further when CO is present in sufficient quantities |
| 443 |
< |
on the surface, ~20 kcal/mole. Once an adatom exists on the surface, its barrier for diffusion is negligible ( < 4 kcal/mole) |
| 444 |
< |
and is well able to explore its terrace. Atoms traversing terraces is more difficult, but can be overcome through a joining and lifting stage. |
| 445 |
< |
By tracking the mobility of individual metal atoms on the Platinum and Gold surfaces we were able to determine |
| 446 |
< |
the relative diffusion rates and how varying coverages of CO affected the rates. Close |
| 447 |
< |
observation of the mobile metal atoms showed that they were typically in equilibrium with the |
| 448 |
< |
step edges, constantly breaking apart and rejoining. Additionally, at times their motion was concerted and |
| 449 |
< |
two or more atoms would be observed moving together across the surfaces. The primary challenge in quantifying |
| 450 |
< |
the overall surface mobility was in defining ``mobile" vs. ``static" atoms. |
| 435 |
> |
\subsubsection{Double layers} |
| 436 |
> |
Tao {\it et al}.\cite{Tao:2010} have shown experimentally that the Pt(557) surface |
| 437 |
> |
undergoes two separate reconstructions upon CO adsorption. |
| 438 |
> |
The first involves a doubling of the step height and plateau length. |
| 439 |
> |
Similar behavior has been seen on a number of surfaces |
| 440 |
> |
at varying conditions, including Ni(977) and Si(111).\cite{Williams:1994,Williams:1991,Pearl} |
| 441 |
> |
Of the two systems we examined, the Pt system showed a greater |
| 442 |
> |
propensity for reconstruction |
| 443 |
> |
because of the larger surface mobility and the greater extent of step wandering. |
| 444 |
> |
The amount of reconstruction was strongly correlated to the amount of CO |
| 445 |
> |
adsorbed upon the surface. This appears to be related to the |
| 446 |
> |
effect that adsorbate coverage has on edge breakup and on the |
| 447 |
> |
surface diffusion of metal adatoms. Only the 50\% Pt surface underwent the |
| 448 |
> |
doubling seen by Tao {\it et al}.\cite{Tao:2010} within the time scales studied here. |
| 449 |
> |
Over a longer time scale (150~ns) two more double layers formed |
| 450 |
> |
on this surface. Although double layer formation did not occur |
| 451 |
> |
in the other Pt systems, they exhibited more step-wandering and |
| 452 |
> |
roughening compared to their Au counterparts. The |
| 453 |
> |
50\% Pt system is highlighted in Figure \ref{fig:reconstruct} at |
| 454 |
> |
various times along the simulation showing the evolution of a double layer step-edge. |
| 455 |
|
|
| 456 |
< |
A particle was considered mobile once it had traveled more than 2~\AA~ between saved configurations |
| 457 |
< |
of the system (10-100 ps). An atom that was truly mobile would typically travel much greater than this, but |
| 458 |
< |
the 2~\AA~ cutoff was to prevent the in-place vibrational movement of atoms from being included in the analysis. |
| 459 |
< |
Since diffusion on a surface is strongly affected by local structures, in this case the presence of single and double |
| 460 |
< |
layer step edges, the diffusion parallel to the step edges was determined separately from the diffusion perpendicular |
| 414 |
< |
to these edges. The parallel and perpendicular diffusion constants are shown in figure \ref{fig:diff}. |
| 456 |
> |
The second reconstruction observed by |
| 457 |
> |
Tao {\it et al}.\cite{Tao:2010} involved the formation of triangular clusters that stretched |
| 458 |
> |
across the plateau between two step-edges. Neither metal, within |
| 459 |
> |
the 40~ns time scale or the extended simulation time of 150~ns for |
| 460 |
> |
the 50\% Pt system, experienced this reconstruction. |
| 461 |
|
|
| 416 |
– |
\subsubsection{Double layer formation} |
| 417 |
– |
The increased amounts of diffusion on Pt at the higher CO coverages appears to play a role in the |
| 418 |
– |
formation of double layers, seeing as how that was the only system within our observed simulation time |
| 419 |
– |
that showed the formation. Despite this being the only system where this reconstruction occurs, three separate layers |
| 420 |
– |
were formed over the extended run time of this system. As mentioned earlier, previous experimental work has given some insight into |
| 421 |
– |
the upper bounds of the time required for enough atoms to move around to allow two steps to coalesce\cite{Williams:1991,Pearl}. |
| 422 |
– |
As seen in figure \ref{fig:reconstruct}, the first appearance of a double layer, a nodal site, appears at 19 ns into |
| 423 |
– |
the simulation. Within 12 ns, nearly half of the step has formed the double layer and by 86 ns, a smooth complete |
| 424 |
– |
layer has formed. The double layer is complete by 37 ns but is a bit rough. |
| 425 |
– |
From the appearance of the first node to the initial doubling of the layers ignoring their roughness took ~20 ns. |
| 426 |
– |
Another ~40 ns was necessary for the layer to completely straighten. The other two layers in this simulation form |
| 427 |
– |
over a period of 22 ns and 42 ns respectively. |
| 428 |
– |
|
| 462 |
|
%Evolution of surface |
| 463 |
|
\begin{figure}[H] |
| 464 |
< |
\includegraphics[width=\linewidth]{ProgressionOfDoubleLayerFormation_yellowCircle.png} |
| 464 |
> |
\includegraphics[width=\linewidth]{EPS_ProgressionOfDoubleLayerFormation} |
| 465 |
|
\caption{The Pt(557) / 50\% CO system at a sequence of times after |
| 466 |
< |
initial exposure to the CO: (a) 258 ps, (b) 19 ns, (c) 31.2 ns, and |
| 467 |
< |
(d) 86.1 ns. Disruption of the 557 step edges occurs quickly. The |
| 468 |
< |
doubling of the layers appears only after two adjacent step edges |
| 466 |
> |
initial exposure to the CO: (a) 258~ps, (b) 19~ns, (c) 31.2~ns, and |
| 467 |
> |
(d) 86.1~ns. Disruption of the (557) step-edges occurs quickly. The |
| 468 |
> |
doubling of the layers appears only after two adjacent step-edges |
| 469 |
|
touch. The circled spot in (b) nucleated the growth of the double |
| 470 |
|
step observed in the later configurations.} |
| 471 |
|
\label{fig:reconstruct} |
| 472 |
|
\end{figure} |
| 473 |
+ |
|
| 474 |
+ |
\subsection{Dynamics} |
| 475 |
+ |
Previous experimental work by Pearl and Sibener\cite{Pearl}, |
| 476 |
+ |
using STM, has been able to capture the coalescence of steps |
| 477 |
+ |
on Ni(977). The time scale of the image acquisition, $\sim$70~s/image, |
| 478 |
+ |
provides an upper bound for the time required for the doubling |
| 479 |
+ |
to occur. By utilizing Molecular Dynamics we are able to probe |
| 480 |
+ |
the dynamics of these reconstructions at elevated temperatures |
| 481 |
+ |
and in this section we provide data on the timescales for transport |
| 482 |
+ |
properties, e.g. diffusion and layer formation time. |
| 483 |
+ |
|
| 484 |
+ |
|
| 485 |
+ |
\subsubsection{Transport of surface metal atoms} |
| 486 |
+ |
%forcedSystems/stepSeparation |
| 487 |
+ |
The wandering of a step-edge is a cooperative effect |
| 488 |
+ |
arising from the individual movements of the atoms making up the steps. An ideal metal surface |
| 489 |
+ |
displaying a low index facet, (111) or (100), is unlikely to experience |
| 490 |
+ |
much surface diffusion because of the large energetic barrier that must |
| 491 |
+ |
be overcome to lift an atom out of the surface. The presence of step-edges and other surface features |
| 492 |
+ |
on higher-index facets provides a lower energy source for mobile metal atoms. |
| 493 |
+ |
Single-atom break-away from a step-edge on a clean surface still imposes an |
| 494 |
+ |
energetic penalty around $\sim$~45 kcal/mol, but this is easier than lifting |
| 495 |
+ |
the same metal atom vertically out of the surface, \textgreater~60 kcal/mol. |
| 496 |
+ |
The penalty lowers significantly when CO is present in sufficient quantities |
| 497 |
+ |
on the surface. For certain distributions of CO, see Discussion, the penalty can fall to as low as |
| 498 |
+ |
$\sim$~20 kcal/mol. Once an adatom exists on the surface, the barrier for |
| 499 |
+ |
diffusion is negligible (\textless~4 kcal/mol for a Pt adatom). These adatoms are then |
| 500 |
+ |
able to explore the terrace before rejoining either their original step-edge or |
| 501 |
+ |
becoming a part of a different edge. It is an energetically unfavorable process with a high barrier for an atom |
| 502 |
+ |
to traverse to a separate terrace although the presence of CO can lower the |
| 503 |
+ |
energy barrier required to lift or lower an adatom. By tracking the mobility of individual |
| 504 |
+ |
metal atoms on the Pt and Au surfaces we were able to determine the relative |
| 505 |
+ |
diffusion constants, as well as how varying coverages of CO affect the diffusion. Close |
| 506 |
+ |
observation of the mobile metal atoms showed that they were typically in |
| 507 |
+ |
equilibrium with the step-edges. |
| 508 |
+ |
At times, their motion was concerted and two or more adatoms would be |
| 509 |
+ |
observed moving together across the surfaces. |
| 510 |
|
|
| 511 |
+ |
A particle was considered ``mobile'' once it had traveled more than 2~\AA~ |
| 512 |
+ |
between saved configurations of the system (typically 10-100 ps). A mobile atom |
| 513 |
+ |
would typically travel much greater distances than this, but the 2~\AA~cutoff |
| 514 |
+ |
was used to prevent swamping the diffusion data with the in-place vibrational |
| 515 |
+ |
movement of buried atoms. Diffusion on a surface is strongly affected by |
| 516 |
+ |
local structures and in this work, the presence of single and double layer |
| 517 |
+ |
step-edges causes the diffusion parallel to the step-edges to be larger than |
| 518 |
+ |
the diffusion perpendicular to these edges. Parallel and perpendicular |
| 519 |
+ |
diffusion constants are shown in Figure \ref{fig:diff}. |
| 520 |
+ |
|
| 521 |
+ |
%Diffusion graph |
| 522 |
|
\begin{figure}[H] |
| 523 |
< |
\includegraphics[width=\linewidth]{DiffusionComparison_errorXY_remade.pdf} |
| 523 |
> |
\includegraphics[width=\linewidth]{Portrait_DiffusionComparison_1} |
| 524 |
|
\caption{Diffusion constants for mobile surface atoms along directions |
| 525 |
|
parallel ($\mathbf{D}_{\parallel}$) and perpendicular |
| 526 |
< |
($\mathbf{D}_{\perp}$) to the 557 step edges as a function of CO |
| 527 |
< |
surface coverage. Diffusion parallel to the step edge is higher |
| 526 |
> |
($\mathbf{D}_{\perp}$) to the (557) step-edges as a function of CO |
| 527 |
> |
surface coverage. Diffusion parallel to the step-edge is higher |
| 528 |
|
than that perpendicular to the edge because of the lower energy |
| 529 |
< |
barrier associated with going from approximately 7 nearest neighbors |
| 530 |
< |
to 5, as compared to the 3 of an adatom. Additionally, the observed |
| 531 |
< |
maximum and subsequent decrease for the Pt system suggests that the |
| 532 |
< |
CO self-interactions are playing a significant role with regards to |
| 533 |
< |
movement of the platinum atoms around and more importantly across |
| 453 |
< |
the surface. } |
| 529 |
> |
barrier associated with traversing along the edge as compared to |
| 530 |
> |
completely breaking away. The two reported diffusion constants for |
| 531 |
> |
the 50\% Pt system arise from different sample sets. The lower values |
| 532 |
> |
correspond to the same 40~ns amount that all of the other systems were |
| 533 |
> |
examined at, while the larger values correspond to a 20~ns period } |
| 534 |
|
\label{fig:diff} |
| 535 |
|
\end{figure} |
| 536 |
|
|
| 537 |
+ |
The weaker Au-CO interaction is evident in the weak CO-coverage |
| 538 |
+ |
dependance of Au diffusion. This weak interaction leads to lower |
| 539 |
+ |
observed coverages when compared to dosage amounts. This further |
| 540 |
+ |
limits the effect the CO can have on surface diffusion. The correlation |
| 541 |
+ |
between coverage and Pt diffusion rates shows a near linear relationship |
| 542 |
+ |
at the earliest times in the simulations. Following double layer formation, |
| 543 |
+ |
however, there is a precipitous drop in adatom diffusion. As the double |
| 544 |
+ |
layer forms, many atoms that had been tracked for mobility data have |
| 545 |
+ |
now been buried resulting in a smaller reported diffusion constant. A |
| 546 |
+ |
secondary effect of higher coverages is CO-CO cross interactions that |
| 547 |
+ |
lower the effective mobility of the Pt adatoms that are bound to each CO. |
| 548 |
+ |
This effect would become evident only at higher coverages. A detailed |
| 549 |
+ |
account of Pt adatom energetics follows in the Discussion. |
| 550 |
+ |
|
| 551 |
|
|
| 552 |
+ |
\subsubsection{Dynamics of double layer formation} |
| 553 |
+ |
The increased diffusion on Pt at the higher CO coverages is the primary |
| 554 |
+ |
contributor to double layer formation. However, this is not a complete |
| 555 |
+ |
explanation -- the 33\%~Pt system has higher diffusion constants, but |
| 556 |
+ |
did not show any signs of edge doubling in 40~ns. On the 50\%~Pt |
| 557 |
+ |
system, one double layer formed within the first 40~ns of simulation time, |
| 558 |
+ |
while two more were formed as the system was allowed to run for an |
| 559 |
+ |
additional 110~ns (150~ns total). This suggests that this reconstruction |
| 560 |
+ |
is a rapid process and that the previously mentioned upper bound is a |
| 561 |
+ |
very large overestimate.\cite{Williams:1991,Pearl} In this system the first |
| 562 |
+ |
appearance of a double layer appears at 19~ns into the simulation. |
| 563 |
+ |
Within 12~ns of this nucleation event, nearly half of the step has formed |
| 564 |
+ |
the double layer and by 86~ns the complete layer has flattened out. |
| 565 |
+ |
From the appearance of the first nucleation event to the first observed |
| 566 |
+ |
double layer, the process took $\sim$20~ns. Another $\sim$40~ns was |
| 567 |
+ |
necessary for the layer to completely straighten. The other two layers in |
| 568 |
+ |
this simulation formed over periods of 22~ns and 42~ns respectively. |
| 569 |
+ |
A possible explanation for this rapid reconstruction is the elevated |
| 570 |
+ |
temperatures under which our systems were simulated. The process |
| 571 |
+ |
would almost certainly take longer at lower temperatures. Additionally, |
| 572 |
+ |
our measured times for completion of the doubling after the appearance |
| 573 |
+ |
of a nucleation site are likely affected by our periodic boxes. A longer |
| 574 |
+ |
step-edge will likely take longer to ``zipper''. |
| 575 |
|
|
| 576 |
|
|
| 577 |
|
%Discussion |
| 578 |
|
\section{Discussion} |
| 579 |
< |
In this paper we have shown that we were able to accurately model the initial reconstruction of the |
| 580 |
< |
Pt (557) surface upon CO adsorption as shown by Tao et al. \cite{Tao:2010}. More importantly, we |
| 581 |
< |
were able to capture the dynamic processes inherent within this reconstruction. |
| 579 |
> |
We have shown that a classical potential is able to model the initial |
| 580 |
> |
reconstruction of the Pt(557) surface upon CO adsorption, and have |
| 581 |
> |
reproduced the double layer structure observed by Tao {\it et |
| 582 |
> |
al}.\cite{Tao:2010}. Additionally, this reconstruction appears to be |
| 583 |
> |
rapid -- occurring within 100 ns of the initial exposure to CO. Here |
| 584 |
> |
we discuss the features of the classical potential that are |
| 585 |
> |
contributing to the stability and speed of the Pt(557) reconstruction. |
| 586 |
|
|
| 587 |
< |
\subsection{Mechanism for restructuring} |
| 588 |
< |
The increased computational cost to examine this system using molecular dynamics rather than |
| 589 |
< |
a Monte Carlo based approach was necessary so that our predictions on possible mechanisms |
| 590 |
< |
and driving forces would have support not only from thermodynamic arguments but also from the |
| 591 |
< |
actual dynamics of the system. |
| 587 |
> |
\subsection{Diffusion} |
| 588 |
> |
The perpendicular diffusion constant appears to be the most important |
| 589 |
> |
indicator of double layer formation. As highlighted in Figure |
| 590 |
> |
\ref{fig:reconstruct}, the formation of the double layer did not begin |
| 591 |
> |
until a nucleation site appeared. Williams {\it et |
| 592 |
> |
al}.\cite{Williams:1991,Williams:1994} cite an effective edge-edge |
| 593 |
> |
repulsion arising from the inability of edge crossing. This repulsion |
| 594 |
> |
must be overcome to allow step coalescence. A larger |
| 595 |
> |
$\textbf{D}_\perp$ value implies more step-wandering and a larger |
| 596 |
> |
chance for the stochastic meeting of two edges to create a nucleation |
| 597 |
> |
point. Diffusion parallel to the step-edge can help ``zipper'' up a |
| 598 |
> |
nascent double layer. This helps explain the rapid time scale for |
| 599 |
> |
double layer completion after the appearance of a nucleation site, while |
| 600 |
> |
the initial appearance of the nucleation site was unpredictable. |
| 601 |
|
|
| 602 |
< |
Comparing the results from simulation to those reported previously by |
| 603 |
< |
Tao et al. the similarities in the platinum and CO system are quite |
| 604 |
< |
strong. As shown in figure \ref{fig:reconstruct}, the simulated platinum system under a CO |
| 605 |
< |
atmosphere will restructure slightly by doubling the terrace |
| 606 |
< |
heights. The restructuring appears to occur slowly, one to two |
| 607 |
< |
platinum atoms at a time. Looking at individual snapshots, these |
| 478 |
< |
adatoms tend to either rise on top of the plateau or break away from |
| 479 |
< |
the step edge and then diffuse perpendicularly to the step direction |
| 480 |
< |
until reaching another step edge. This combination of growth and decay |
| 481 |
< |
of the step edges appears to be in somewhat of a state of dynamic |
| 482 |
< |
equilibrium. However, once two previously separated edges meet as |
| 483 |
< |
shown in figure 1.B, this point tends to act as a focus or growth |
| 484 |
< |
point for the rest of the edge to meet up, akin to that of a |
| 485 |
< |
zipper. From the handful of cases where a double layer was formed |
| 486 |
< |
during the simulation, measuring from the initial appearance of a |
| 487 |
< |
growth point, the double layer tends to be fully formed within |
| 488 |
< |
$\sim$~35 ns. |
| 489 |
< |
|
| 490 |
< |
There are a number of possible mechanisms to explain the role of |
| 491 |
< |
adsorbed CO in restructuring the Pt surface. Quadrupolar repulsion |
| 492 |
< |
between adjacent CO molecules adsorbed on the surface is one |
| 602 |
> |
\subsection{Mechanism for restructuring} |
| 603 |
> |
Since the Au surface showed no large scale restructuring in any of our |
| 604 |
> |
simulations, our discussion will focus on the 50\% Pt-CO system which |
| 605 |
> |
did exhibit doubling. A number of possible mechanisms exist to explain |
| 606 |
> |
the role of adsorbed CO in restructuring the Pt surface. Quadrupolar |
| 607 |
> |
repulsion between adjacent CO molecules adsorbed on the surface is one |
| 608 |
|
possibility. However, the quadrupole-quadrupole interaction is |
| 609 |
|
short-ranged and is attractive for some orientations. If the CO |
| 610 |
< |
molecules are ``locked'' in a specific orientation relative to each other however, |
| 611 |
< |
this explanation gains some weight. The energetic repulsion between two CO |
| 612 |
< |
located a distance of 2.77~\AA~apart (nearest-neighbor distance of Pt) with both in a |
| 613 |
< |
vertical orientation is 8.62 kcal/mole. Moving the CO apart to the second nearest-neighbor |
| 614 |
< |
distance of 4.8~\AA~or 5.54~\AA~drops the repulsion to nearly 0 kcal/mole. SHOW A NUMBER FOR ROTATION. |
| 615 |
< |
As mentioned above, the energy barrier for surface diffusion of a platinum adatom is only 4 kcal/mole. So this |
| 616 |
< |
repulsion between CO can help increase the surface diffusion. However, the residence time of CO was examined |
| 617 |
< |
and while the majority of the CO is on or near the surface throughout the run, it is extremely mobile. This mobility |
| 618 |
< |
suggests that the CO are more likely to shift their positions without necessarily dragging the platinum along |
| 619 |
< |
with them. |
| 610 |
> |
molecules are ``locked'' in a vertical orientation, through atop |
| 611 |
> |
adsorption for example, this explanation would gain credence. The |
| 612 |
> |
calculated energetic repulsion between two CO molecules located a |
| 613 |
> |
distance of 2.77~\AA~apart (nearest-neighbor distance of Pt) and both |
| 614 |
> |
in a vertical orientation, is 8.62 kcal/mol. Moving the CO to the |
| 615 |
> |
second nearest-neighbor distance of 4.8~\AA~drops the repulsion to |
| 616 |
> |
nearly 0. Allowing the CO to rotate away from a purely vertical |
| 617 |
> |
orientation also lowers the repulsion. When the carbons are locked at |
| 618 |
> |
a distance of 2.77~\AA, a minimum of 6.2 kcal/mol is reached when the |
| 619 |
> |
angle between the 2 CO is $\sim$24\textsuperscript{o}. The calculated |
| 620 |
> |
barrier for surface diffusion of a Pt adatom is only 4 kcal/mol, so |
| 621 |
> |
repulsion between adjacent CO molecules bound to Pt could increase the |
| 622 |
> |
surface diffusion. However, the residence time of CO on Pt suggests |
| 623 |
> |
that the CO molecules are extremely mobile, with diffusion constants 40 |
| 624 |
> |
to 2500 times larger than surface Pt atoms. This mobility suggests |
| 625 |
> |
that the CO molecules jump between different Pt atoms throughout the |
| 626 |
> |
simulation, but can stay bound for significant periods of time. |
| 627 |
|
|
| 628 |
< |
Another possible and more likely mechanism for the restructuring is in the |
| 629 |
< |
destabilization of strong Pt-Pt interactions by CO adsorbed on surface |
| 630 |
< |
Pt atoms. This could have the effect of increasing surface mobility |
| 631 |
< |
of these atoms. To test this hypothesis, numerous configurations of |
| 632 |
< |
CO in varying quantities were arranged on the higher and lower plateaus |
| 633 |
< |
around a step on a otherwise clean Pt (557) surface. One representative |
| 634 |
< |
configuration is displayed in figure \ref{fig:lambda}. Single or concerted movement |
| 635 |
< |
of platinum atoms was then examined to determine possible barriers. Because |
| 636 |
< |
of the forced movement along a pre-defined reaction coordinate that may differ |
| 637 |
< |
from the true minimum of this path, only the beginning and ending energies |
| 638 |
< |
are displayed in table \ref{tab:energies}. The presence of CO at suitable |
| 639 |
< |
sites can lead to lowered barriers for platinum breaking apart from the step edge. |
| 640 |
< |
Additionally, as highlighted in figure \ref{fig:lambda}, the presence of CO makes the |
| 641 |
< |
burrowing and lifting nature favorable, whereas without CO, the process is neutral |
| 642 |
< |
in terms of energetics. |
| 628 |
> |
A different interpretation of the above mechanism which takes the |
| 629 |
> |
large mobility of the CO into account, would be in the destabilization |
| 630 |
> |
of Pt-Pt interactions due to bound CO. Destabilizing Pt-Pt bonds at |
| 631 |
> |
the edges could lead to increased step-edge breakup and diffusion. On |
| 632 |
> |
the bare Pt(557) surface the barrier to completely detach an edge atom |
| 633 |
> |
is $\sim$43~kcal/mol, as is shown in configuration (a) in Figures |
| 634 |
> |
\ref{fig:SketchGraphic} \& \ref{fig:SketchEnergies}. For certain |
| 635 |
> |
configurations, cases (e), (g), and (h), the barrier can be lowered to |
| 636 |
> |
$\sim$23~kcal/mol by the presence of bound CO molecules. In these |
| 637 |
> |
instances, it becomes energetically favorable to roughen the edge by |
| 638 |
> |
introducing a small separation of 0.5 to 1.0~\AA. This roughening |
| 639 |
> |
becomes immediately obvious in simulations with significant CO |
| 640 |
> |
populations. The roughening is present to a lesser extent on surfaces |
| 641 |
> |
with lower CO coverage (and even on the bare surfaces), although in |
| 642 |
> |
these cases it is likely due to random fluctuations that squeeze out |
| 643 |
> |
step-edge atoms. Step-edge breakup by continuous single-atom |
| 644 |
> |
translations (as suggested by these energy curves) is probably a |
| 645 |
> |
worst-case scenario. Multistep mechanisms in which an adatom moves |
| 646 |
> |
laterally on the surface after being ejected would be more |
| 647 |
> |
energetically favorable. This would leave the adatom alongside the |
| 648 |
> |
ledge, providing it with 5 nearest neighbors. While fewer than the 7 |
| 649 |
> |
neighbors it had as part of the step-edge, it keeps more Pt neighbors |
| 650 |
> |
than the 3 an isolated adatom would have on the terrace. In this |
| 651 |
> |
proposed mechanism, the CO quadrupolar repulsion still plays a role in |
| 652 |
> |
the initial roughening of the step-edge, but not in any long-term |
| 653 |
> |
bonds with individual Pt atoms. Higher CO coverages create more |
| 654 |
> |
opportunities for the crowded CO configurations shown in Figure |
| 655 |
> |
\ref{fig:SketchGraphic}, and this is likely to cause an increased |
| 656 |
> |
propensity for step-edge breakup. |
| 657 |
|
|
| 658 |
+ |
%Sketch graphic of different configurations |
| 659 |
+ |
\begin{figure}[H] |
| 660 |
+ |
\includegraphics[width=\linewidth]{COpaths} |
| 661 |
+ |
\caption{Configurations used to investigate the mechanism of step-edge |
| 662 |
+ |
breakup on Pt(557). In each case, the central (starred) atom is |
| 663 |
+ |
pulled directly across the surface away from the step edge. The Pt |
| 664 |
+ |
atoms on the upper terrace are colored dark grey, while those on the |
| 665 |
+ |
lower terrace are in white. In each of these configurations, some |
| 666 |
+ |
number of the atoms (highlighted in blue) had a CO molecule bound in |
| 667 |
+ |
a vertical atop position. The energies of these configurations as a |
| 668 |
+ |
function of central atom displacement are displayed in Figure |
| 669 |
+ |
\ref{fig:SketchEnergies}.} |
| 670 |
+ |
\label{fig:SketchGraphic} |
| 671 |
+ |
\end{figure} |
| 672 |
+ |
|
| 673 |
+ |
%energy graph corresponding to sketch graphic |
| 674 |
+ |
\begin{figure}[H] |
| 675 |
+ |
\includegraphics[width=\linewidth]{Portrait_SeparationComparison} |
| 676 |
+ |
\caption{Energies for displacing a single edge atom perpendicular to |
| 677 |
+ |
the step edge as a function of atomic displacement. Each of the |
| 678 |
+ |
energy curves corresponds to one of the labeled configurations in |
| 679 |
+ |
Figure \ref{fig:SketchGraphic}, and are referenced to the |
| 680 |
+ |
unperturbed step-edge. Certain arrangements of bound CO (notably |
| 681 |
+ |
configurations g and h) can lower the energetic barrier for creating |
| 682 |
+ |
an adatom relative to the bare surface (configuration a).} |
| 683 |
+ |
\label{fig:SketchEnergies} |
| 684 |
+ |
\end{figure} |
| 685 |
+ |
|
| 686 |
+ |
While configurations of CO on the surface are able to increase |
| 687 |
+ |
diffusion and the likelihood of edge wandering, this does not provide |
| 688 |
+ |
a complete explanation for the formation of double layers. If adatoms |
| 689 |
+ |
were constrained to their original terraces then doubling could not |
| 690 |
+ |
occur. A mechanism for vertical displacement of adatoms at the |
| 691 |
+ |
step-edge is required to explain the doubling. |
| 692 |
+ |
|
| 693 |
+ |
We have discovered one possible mechanism for a CO-mediated vertical |
| 694 |
+ |
displacement of Pt atoms at the step edge. Figure \ref{fig:lambda} |
| 695 |
+ |
shows four points along a reaction coordinate in which a CO-bound |
| 696 |
+ |
adatom along the step-edge ``burrows'' into the edge and displaces the |
| 697 |
+ |
original edge atom onto the higher terrace. A number of events similar |
| 698 |
+ |
to this mechanism were observed during the simulations. We predict an |
| 699 |
+ |
energetic barrier of 20~kcal/mol for this process (in which the |
| 700 |
+ |
displaced edge atom follows a curvilinear path into an adjacent 3-fold |
| 701 |
+ |
hollow site). The barrier heights we obtain for this reaction |
| 702 |
+ |
coordinate are approximate because the exact path is unknown, but the |
| 703 |
+ |
calculated energy barriers would be easily accessible at operating |
| 704 |
+ |
conditions. Additionally, this mechanism is exothermic, with a final |
| 705 |
+ |
energy 15~kcal/mol below the original $\lambda = 0$ configuration. |
| 706 |
+ |
When CO is not present and this reaction coordinate is followed, the |
| 707 |
+ |
process is endothermic by 3~kcal/mol. The difference in the relative |
| 708 |
+ |
energies for the $\lambda=0$ and $\lambda=1$ case when CO is present |
| 709 |
+ |
provides strong support for CO-mediated Pt-Pt interactions giving rise |
| 710 |
+ |
to the doubling reconstruction. |
| 711 |
+ |
|
| 712 |
|
%lambda progression of Pt -> shoving its way into the step |
| 713 |
|
\begin{figure}[H] |
| 714 |
< |
\includegraphics[width=\linewidth]{lambdaProgression_atopCO.png} |
| 715 |
< |
\caption{A model system of the Pt 557 surface was used as the framework for a reaction coordinate. |
| 716 |
< |
Various numbers, placements, and rotations of CO were examined. The one displayed was a |
| 717 |
< |
representative sample. As shown in Table , relative to the energy at 0\% there is a slight decrease |
| 718 |
< |
upon insertion of the platinum atom into the step edge along with the resultant lifting of the other |
| 719 |
< |
platinum atom.} |
| 714 |
> |
\includegraphics[width=\linewidth]{EPS_rxnCoord} |
| 715 |
> |
\caption{Points along a possible reaction coordinate for CO-mediated |
| 716 |
> |
edge doubling. Here, a CO-bound adatom burrows into an established |
| 717 |
> |
step edge and displaces an edge atom onto the upper terrace along a |
| 718 |
> |
curvilinear path. The approximate barrier for the process is |
| 719 |
> |
20~kcal/mol, and the complete process is exothermic by 15~kcal/mol |
| 720 |
> |
in the presence of CO, but is endothermic by 3~kcal/mol without.} |
| 721 |
|
\label{fig:lambda} |
| 722 |
|
\end{figure} |
| 723 |
|
|
| 724 |
+ |
The mechanism for doubling on the Pt(557) surface appears to require |
| 725 |
+ |
the cooperation of at least two distinct processes. For complete |
| 726 |
+ |
doubling of a layer to occur there must be a breakup of one |
| 727 |
+ |
terrace. These atoms must then ``disappear'' from that terrace, either |
| 728 |
+ |
by travelling to the terraces above of below their original levels. |
| 729 |
+ |
The presence of CO helps explain mechanisms for both of these |
| 730 |
+ |
situations. There must be sufficient breakage of the step-edge to |
| 731 |
+ |
increase the concentration of adatoms on the surface and these adatoms |
| 732 |
+ |
must then undergo the burrowing highlighted above (or a comparable |
| 733 |
+ |
mechanism) to create the double layer. With sufficient time, these |
| 734 |
+ |
mechanisms working in concert lead to the formation of a double layer. |
| 735 |
|
|
| 736 |
+ |
\subsection{CO Removal and double layer stability} |
| 737 |
+ |
Once a double layer had formed on the 50\%~Pt system, it remained for |
| 738 |
+ |
the rest of the simulation time with minimal movement. Random |
| 739 |
+ |
fluctuations that involved small clusters or divots were observed, but |
| 740 |
+ |
these features typically healed within a few nanoseconds. Within our |
| 741 |
+ |
simulations, the formation of the double layer appeared to be |
| 742 |
+ |
irreversible and a double layer was never observed to split back into |
| 743 |
+ |
two single layer step-edges while CO was present. |
| 744 |
|
|
| 745 |
< |
\subsection{Diffusion} |
| 746 |
< |
As shown in the results section, the diffusion parallel to the step edge tends to be |
| 747 |
< |
much faster than that perpendicular to the step edge. Additionally, the coverage |
| 748 |
< |
of CO appears to play a slight role in relative rates of diffusion, as shown in figure \ref{fig:diff} |
| 749 |
< |
Thus, the bottleneck of the double layer formation appears to be the initial formation |
| 750 |
< |
of this growth point, which seems to be somewhat of a stochastic event. Once it |
| 751 |
< |
appears, parallel diffusion, along the now slightly angled step edge, will allow for |
| 752 |
< |
a faster formation of the double layer than if the entire process were dependent on |
| 753 |
< |
only perpendicular diffusion across the plateaus. Thus, the larger $D_{\perp}$, the |
| 754 |
< |
more likely a growth point is to be formed. |
| 755 |
< |
\\ |
| 745 |
> |
To further gauge the effect CO has on this surface, additional |
| 746 |
> |
simulations were run starting from a late configuration of the 50\%~Pt |
| 747 |
> |
system that had already formed double layers. These simulations then |
| 748 |
> |
had their CO forcibly removed. The double layer broke apart rapidly |
| 749 |
> |
in these simulations, showing a well-defined edge-splitting after |
| 750 |
> |
100~ps. Configurations of this system are shown in Figure |
| 751 |
> |
\ref{fig:breaking}. The coloring of the top and bottom layers helps to |
| 752 |
> |
exhibit how much mixing the edges experience as they split. These |
| 753 |
> |
systems were only examined for 10~ns, and within that time despite the |
| 754 |
> |
initial rapid splitting, the edges only moved another few |
| 755 |
> |
\AA~apart. It is possible that with longer simulation times, the (557) |
| 756 |
> |
surface recovery observed by Tao {\it et al}.\cite{Tao:2010} could |
| 757 |
> |
also be recovered. |
| 758 |
|
|
| 547 |
– |
|
| 759 |
|
%breaking of the double layer upon removal of CO |
| 760 |
|
\begin{figure}[H] |
| 761 |
< |
\includegraphics[width=\linewidth]{doubleLayerBreaking_greenBlue_whiteLetters.png} |
| 762 |
< |
\caption{Hi} |
| 761 |
> |
\includegraphics[width=\linewidth]{EPS_doubleLayerBreaking} |
| 762 |
> |
\caption{Dynamics of an established (111) double step after removal of |
| 763 |
> |
the adsorbed CO: (A) 0~ps, (B) 100~ps, and (C) 1~ns after the removal |
| 764 |
> |
of CO. The presence of the CO helped maintain the stability of the |
| 765 |
> |
double step. Nearly immediately after the CO is removed, the step |
| 766 |
> |
edge reforms in a (100) configuration, which is also the step type |
| 767 |
> |
seen on clean (557) surfaces. The step separation involves |
| 768 |
> |
significant mixing of the lower and upper atoms at the edge.} |
| 769 |
|
\label{fig:breaking} |
| 770 |
|
\end{figure} |
| 771 |
|
|
| 772 |
|
|
| 556 |
– |
|
| 557 |
– |
|
| 773 |
|
%Peaks! |
| 774 |
< |
\begin{figure}[H] |
| 775 |
< |
\includegraphics[width=\linewidth]{doublePeaks_noCO.png} |
| 776 |
< |
\caption{} |
| 777 |
< |
\label{fig:peaks} |
| 778 |
< |
\end{figure} |
| 774 |
> |
%\begin{figure}[H] |
| 775 |
> |
%\includegraphics[width=\linewidth]{doublePeaks_noCO.png} |
| 776 |
> |
%\caption{At the initial formation of this double layer ( $\sim$ 37 ns) there is a degree |
| 777 |
> |
%of roughness inherent to the edge. The next $\sim$ 40 ns show the edge with |
| 778 |
> |
%aspects of waviness and by 80 ns the double layer is completely formed and smooth. } |
| 779 |
> |
%\label{fig:peaks} |
| 780 |
> |
%\end{figure} |
| 781 |
|
|
| 782 |
+ |
|
| 783 |
+ |
%Don't think I need this |
| 784 |
|
%clean surface... |
| 785 |
< |
\begin{figure}[H] |
| 786 |
< |
\includegraphics[width=\linewidth]{557_300K_cleanPDF.pdf} |
| 787 |
< |
\caption{} |
| 785 |
> |
%\begin{figure}[H] |
| 786 |
> |
%\includegraphics[width=\linewidth]{557_300K_cleanPDF} |
| 787 |
> |
%\caption{} |
| 788 |
|
|
| 789 |
< |
\end{figure} |
| 790 |
< |
\label{fig:clean} |
| 789 |
> |
%\end{figure} |
| 790 |
> |
%\label{fig:clean} |
| 791 |
> |
|
| 792 |
> |
|
| 793 |
|
\section{Conclusion} |
| 794 |
+ |
The strength and directionality of the Pt-CO binding interaction, as |
| 795 |
+ |
well as the large quadrupolar repulsion between atop-bound CO |
| 796 |
+ |
molecules, help to explain the observed increase in surface mobility |
| 797 |
+ |
of Pt(557) and the resultant reconstruction into a double-layer |
| 798 |
+ |
configuration at the highest simulated CO-coverages. The weaker Au-CO |
| 799 |
+ |
interaction results in significantly lower adataom diffusion |
| 800 |
+ |
constants, less step-wandering, and a lack of the double layer |
| 801 |
+ |
reconstruction on the Au(557) surface. |
| 802 |
|
|
| 803 |
+ |
An in-depth examination of the energetics shows the important role CO |
| 804 |
+ |
plays in increasing step-breakup and in facilitating edge traversal |
| 805 |
+ |
which are both necessary for double layer formation. |
| 806 |
|
|
| 807 |
|
%Things I am not ready to remove yet |
| 808 |
|
|
| 826 |
|
% \end{tabular} |
| 827 |
|
% \end{table} |
| 828 |
|
|
| 829 |
< |
\section{Acknowledgments} |
| 830 |
< |
Support for this project was provided by the National Science |
| 831 |
< |
Foundation under grant CHE-0848243 and by the Center for Sustainable |
| 832 |
< |
Energy at Notre Dame (cSEND). Computational time was provided by the |
| 833 |
< |
Center for Research Computing (CRC) at the University of Notre Dame. |
| 834 |
< |
|
| 829 |
> |
\begin{acknowledgement} |
| 830 |
> |
We gratefully acknowledge conversations with Dr. William |
| 831 |
> |
F. Schneider and Dr. Feng Tao. Support for this project was |
| 832 |
> |
provided by the National Science Foundation under grant CHE-0848243 |
| 833 |
> |
and by the Center for Sustainable Energy at Notre Dame |
| 834 |
> |
(cSEND). Computational time was provided by the Center for Research |
| 835 |
> |
Computing (CRC) at the University of Notre Dame. |
| 836 |
> |
\end{acknowledgement} |
| 837 |
|
\newpage |
| 838 |
|
\bibliography{firstTryBibliography} |
| 839 |
< |
\end{doublespace} |
| 839 |
> |
%\end{doublespace} |
| 840 |
> |
|
| 841 |
> |
\begin{tocentry} |
| 842 |
> |
%\includegraphics[height=3.5cm]{timelapse} |
| 843 |
> |
\includegraphics[height=3.5cm]{TOC_doubleLayer.pdf} |
| 844 |
> |
\end{tocentry} |
| 845 |
> |
|
| 846 |
|
\end{document} |
