Letter
pubs.acs.org/NanoLett
Synthesis of MoS2 and MoSe2 Films with Vertically Aligned Layers
Desheng Kong,† Haotian Wang,‡ Judy J. Cha,† Mauro Pasta,† Kristie J. Koski,† Jie Yao,† and Yi Cui*,†,§
†
Department of Materials Science and Engineering, Stanford University, Stanford, California 94305, United States
Department of Applied Physics, Stanford University, Stanford, California 94305, United States
§
Stanford Institute for Materials and Energy Sciences, SLAC National Accelerator Laboratory, 2575 Sand Hill Road, Menlo Park,
California 94025, United States
‡
S Supporting Information
*
ABSTRACT: Layered materials consist of molecular layers
stacked together by weak interlayer interactions. They often
crystallize to form atomically smooth thin films, nanotubes,
and platelet or fullerene-like nanoparticles due to the
anisotropic bonding. Structures that predominately expose
edges of the layers exhibit high surface energy and are often
considered unstable. In this communication, we present a
synthesis process to grow MoS2 and MoSe2 thin films with
vertically aligned layers, thereby maximally exposing the edges
on the film surface. Such edge-terminated films are metastable
structures of MoS2 and MoSe2, which may find applications in
diverse catalytic reactions. We have confirmed their catalytic activity in a hydrogen evolution reaction (HER), in which the
exchange current density correlates directly with the density of the exposed edge sites.
KEYWORDS: Layered materials, MoS2, MoSe2, hydrogen evolution reaction, sulfurization, selenization
L
disulfide (MoS2) and molybdenum diselenide (MoSe2), in
which the molecular layers are aligned vertically to maximally
expose the edges. We find that these films are stable HER
catalysts with large exchange current densities. MoSe2,
introduced here as a novel HER catalyst, exhibits comparable
catalytic activity to MoS2.
MoS2 and MoSe2 share similar crystal structures where the
two-dimensional molecular layers are linked by van der Waals
interaction, as shown in Figure 1a. Each charge-neutral layer
consists of three covalently bonded atomic sheets, for example
S−Mo−S in MoS2, with a layer-to-layer distance of about 6 Å.
Two general types of surface sites are present on these crystals:
terrace sites on the basal planes and edge sites on the side
surfaces. Due to the anisotropic bonding and the general
tendency to minimize the surface energy, nanoparticles of layer
materials usually exhibit platelet-like morphology, in which the
basal planes are exposed, as shown schematically in Figure 1b
(left).7,22,38,42 Alternatively, fullerene-like nanoparticles and
inorganic nanotubes can also form by folding the layers, as
illustrated in Figure 1b (right). Such completely closed
structures have been also obtained in experiments and wellexplained with the surface energy arguments.24−26,33,43 A
conceptually distinctive structure would be one in which the
entire surface area is covered with the edges. It can be achieved
by vertically aligning the layers with respect to the film, as
illustrated in Figure 1c, thereby maximally exposing the edge
ayered materials consist of planar, two-dimensional
molecular layers stacked together by weak interlayer
interactions. Each layer is formed by strong chemical bonding.
The highly anisotropic structure allows top-down exfoliation to
obtain ultrathin flakes by mechanical or chemical processes,1−11
and bottom-up synthesis of thin films, nanoplates, nanoribbons,
inorganic nanotubes, and fullerene-like nanoparticles.12−26 In
reduced dimensions, it is scientifically intriguing to study
nanostructures of layered material as their electronic structures
are often distinctive from their bulk counterpart.3,27−29 Layered
materials usually expose the basal planes as the terminating
surface with minimal roughness and dangling bonds, which are
ideal for electronic device applications.30−32 Another form of
layered materials is the three-dimensional closed nanotube and
fullerene-like nanoparticle, which is attractive as a solid
lubricant and electronic material.26,33 In contrast, less effort
has been made to use the edges of these layered materials. The
edges are full of dangling bonds and chemically active to
manipulate the properties of the layered materials, for example
in n-type doping for graphene.34 In addition, the edges of
layered materials are also the active sites for many important
catalytic reactions, such as hydrodesulfurization,35,36 hydrogen
evolution reaction (HER),37,38 oxygen reduction reactions,39
and methane conversion.40 However, edges are usually the rare
surface sites of layered materials due to their inherently high
surface energy. Increasing the edge dimension is therefore
challenging. 41 Here, we develop a rapid sulfurization/
selenization process to convert Mo thin films into polycrystalline molybdenum dichalcogenide films, including molybdenum
© XXXX American Chemical Society
Received: January 21, 2013
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the terrace sites by 2 orders of magnitude.44 Here, we
demonstrate that the edge-terminated structure can be
synthesized on diverse substrates through a kinetically
controlled rapid growth method.
The molybdenum chalcogenide films are converted from ebeam evaporated, ultrathin Mo films (∼5 nm thick) by a rapid
sulfurization/selenization process in a horizontal tube furnace,
where elemental sulfur/selenium powders are used as the
precursors. The synthesis setup schematic is illustrated in
Figure 2a. This process yields smooth and uniform films as
shown in Figure 2b, which is further confirmed by atomic force
microscopy (AFM) measurements (Supporting Information
Table S9). We employ transmission electron microscopy
(TEM) tomography to reconstruct the three-dimensional
(3D) structure of a representative MoS2 film. Developments
in electron tomography allow the three-dimensional visualization and analysis of materials at nanometer scale along
arbitrary viewing directions.45−48 Here, aberration-corrected
TEM images were acquired for the tomography tilt series to
achieve the highest resolution possible in the reconstructed data
set (Supporting Information, Figure S1). Every tilt image
clearly shows the contrast fringes of individual layers. In Figure
2c, the tomogram reveals domains of striped patterns where the
stripes span from the top surface to the bottom surface of the
film (Supporting Information Movies S11 and S12 display the
cross sections of the reconstructed MoS2 film sequentially to
show the resolved layers throughout the film thickness at
different viewing angles). The spacing between the stripes is
∼6.3 Å, which is consistent with the interlayer spacing of MoS2.
Thus, we confirm that the whole film is terminated by MoS2
edges. A statistical analysis of the tilt angles of the vertical layers
in different domains, obtained from the cross sections of the
reconstructed data, shows that the MoS2 layers are predom-
Figure 1. Nanostructures of layered MoS2 and MoSe2. (a) Layered
crystal structure of molybdenum chalcogenide with individual S−Mo−
S (or Se−Mo−Se) layers stacked along the c-axis by weak van der
Waals interaction. The highly anisotropic crystal structure is the origin
of anisotropic electrical and chemical properties. (b) Schematics of
MoS2 nanoparticle with platelet-like morphology distributed on a
substrate (left), and nanotubes and fullerene-like nanotubes of MoS2
and MoSe2 (right). (c) Idealized structure of edge-terminated
molybdenum chalcogenide films with the layers aligned perpendicular
to the substrate, maximally exposing the edges of the layers.
sites. As a metastable structure, such an edge-terminated film
has been often considered unstable. In the case of MoS2 and
MoSe2, the surface energy of the edge sites is larger than that of
Figure 2. Synthesis setup and as-grown films. (a) Schematic of the synthesis setup in a horizontal tube furnace. (b) Digital photos of a pristine
oxidized silicon (300 nm SiO2/Si) substrate (left), a MoS2 film on oxidized silicon (middle), and a MoSe2 film on oxidized silicon (right). Each
substrate is about 1.5 × 1.5 cm2 in dimension. (c) Volume-rendered reconstructed TEM tomogram of a MoS2 film grown by rapid sulfurization,
which resembles the ideal edge-terminated structure. Individual layers are clearly resolved in this volume-rendered image, with the interlayer spacing
of about 6.3 Å. Movies S1 and S2 display the cross sections of the reconstructed MoS2 film moving throughout the film thickness. (d) Statistical
distribution of tilt angles (θ) of layers in individual grains in edge-terminated MoS2 film, where the tilt angle is defined in the inset. The statistics
include all grains in the reconstructed tomogram.
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inantly aligned perpendicular to the film (Figure 2d, Supporting
Information Figure S2). The film therefore resembles the
proposed structure in Figure 1c which maximally exposes the
edge sites on the surface.
Further structural characterizations provide additional insights into these films. Figure 3a shows a typical TEM image of
Figure 4. (a) TEM image of a MoSe2 film produced by rapid
selenization showing exposed edges. Corresponding high-resolution
TEM image (inset) reveals individual layers consisting of Se−Mo−Se
atomic planes. (b) Raman spectra from edge-terminated MoSe2 films
grown on glassy carbon (GC), quartz, and oxidized silicon (300 nm
SiO2/Si) substrates, respectively.
A sulfurization process was previously used to produce
layered chalcogenide such as MoS2 and WS2, but predominantly with exposed low-energy terraces.50 Such process has
also been widely employed to produce inorganic nanotubes and
fullerene-like nanoparticles.24,25 The distinction can be partially
understood based on previous studies on chalcogenide film
synthesis. It was noticed that the sulfurization/selenization
conditions largely affect the layer orientations in the film.51,52
The formation of the vertically aligned layers in our case is
likely to be driven by kinetic process as illustrated in Figure 5.
Figure 3. (a) TEM image of a MoS2 film produced by rapid
sulfurization, clearly showing exposed edges. High-resolution TEM
image (inset) reveals individual layers consisting of three atomic planes
in the sequence of S−Mo−S. (b) Raman spectra from MoS2 films
grown on glassy carbon (GC), quartz, and oxidized silicon (300 nm
SiO2/Si) substrates, respectively. (c) Schematics of preferentially
excited A1g Raman mode for edge-terminated film (top), and E12g
mode for terrace-terminated film (bottom). (d) Raman spectrum from
a terrace-terminated surface of a MoS2 single crystal.
MoS2 film with densely packed, stripe-like grains. Each grain is
about 10 nm long and several nanometers wide. In the inset of
Figure 3a, the high-resolution TEM image on a single grain
reveals individual atomic planes ordered in the S−Mo−S
sequence to form each layer. The unique edge-terminated
MoS2 films can be grown on various substrates using the same
growth procedure. Figure 3b presents Raman spectra collected
from MoS2 films grown on glassy carbon (GC), quartz, and
oxidized silicon (300 nm SiO2/Si). All three spectra show
consistent spectral features. Notice that the Raman peak
corresponding to the out-of plane Mo−S phonon mode (A1g) is
preferentially excited for edge-terminated film due to the
polarization dependence, whereas the in-plane Mo−S phonon
mode (E12g) is preferentially excited for terrace-terminated
film,49 as illustrated in Figure 3c. Accordingly, the relative
integrated intensities between the two Raman modes provide
texture information of the film. As a reference, the Raman
spectrum from a terrace surface of MoS2 single crystal is shown
in Figure 3d, with the intensity of E12g mode close to that of A1g
mode, in sharp contrast to the spectra of edge-terminated films
with a small E12g peak about 30% of A1g peak. Similarly, TEM
and Raman studies on MoSe2 films, shown in Figure 4a and b,
confirm nearly vertically aligned layers. The dimensions of
individual grains in MoSe2 films are about 20 nm long and
several nanometers wide, slightly larger than those in MoS2
films.
Figure 5. Schematic of the proposed synthesis mechanism. The
sulfurization/selenization reaction requires the diffusion of sulfur/
selenium into the film and converts it into sulfide/selenide. Mass
transport along the layers through van der Waals gaps is much faster
than across the layers in MoS2/MoSe2. Consequently, the layers tend
to be perpendicular to the substrate, with exposed van der Waals gaps
for fast reaction.
During the sulfurization/selenization, sulfur/selenium vapor
diffuses into Mo film and converts it into sulfide/selenide. At
high temperature, the chemical conversion occurs much faster
than the diffusion of sulfur/selenium gas into the film, thereby
making sulfur/selenium diffusion as the rate-limiting process.
Due to the anisotropic structure of MoS2/MoSe2, diffusion
along the layers through van der Waals gaps is expected to be
much faster than diffusion across the layers. Accordingly, the
layers naturally orient perpendicular to the film, exposing van
der Waals gaps for fast reaction. Additional experiments are still
required to figure out the critical factors that control the layer
orientation. We suspect the different sulfurizing precursors,
elemental S used here with respect to hydrogen sulfide (H2S)
in other studies,25,41,50 may account for the difference. Thermal
annealing experiments discussed in later section further
strengthen the proposed kinetically driven growth process.
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The edge terminated film is an attractive candidate material
for catalysis. In particular, the benefits of these films as
electrochemical HER catalysts lie in following aspects. The
films offer the maximal edge sites over a given specific area, and
HER activity is driven by these edge sites.37,38 In addition, the
structure of the film guarantees efficient charge flow from the
conductive support to active surface sites along individual
layers. It is in fact a general consideration in designing MoS2
HER catalysts to minimizing ohmic loss,53,54 as the interlayer
conductivity is 2 orders of magnitude lower than intralayer
conductivity.55,56 Here, we evaluate the catalytic activity of
edge-terminated MoS2 and MoSe2 films based on samples
grown on mirror-polished glassy carbon substrates. Glassy
carbon is the ideal substrate, thanks to its negligible HER
activity in the measurement voltage range and chemical stability
in corrosive electrolyte. Measurements are performed in a 0.5
M H2SO4 solution using a typical three-electrode cell setup (see
Methods). Electrochemical impedance spectroscopy (EIS)
reveals negligible ohmic resistance of these films (Supporting
Information, Figure S5), consistent with the expected efficient
intralayer charge transport. Typical cathodic polarization curves
and corresponding Tafel plots are shown in Figure 6a and b
Table 1. TOFs of the Active Edge Site on Edge-Terminated
MoS2 and MoSe2 Filmsa
materials
exchange current density
(A/cm2)
exchange current per site
(A/site)
TOF
(s−1)
MoS2
MoSe2
2.2 × 10−6
2.0 × 10−6
4.1 × 10−21
4.5 × 10−21
0.013
0.014
a
The lattice parameters from reference X-ray diffraction patterns (PDF
cards no. 00-037-1492 for MoS2 and 04-004-8782 for MoSe2) are used
to calculate the densities of active sites. We use the interlayer distance
instead of the layer spacing on the film to simplify the calculation
(Supporting Information, Fig. S2 and discussion therein).
in situ studies on nanoparticulate catalyst is significant. It
confirms that nearly all of the surface sites on edge-terminated
films are catalytically active. Due to the increased number of
edge sites, the exchange current densities of edge-terminated
films are about ten times higher than previous MoS 2
nanoparticle-based electrodes38 and compare favorably to
most common metal catalysts.57 The similar HER activity
between MoSe2 and MoS2 suggests the Mo atoms are likely the
main active centers on the edges, as already observed in the
hydrodesulfurization reaction.58 This conclusion is further
supported by the general observation of HER activities for
MoS2 edges,37,38 amorphous MoSx films,59 incomplete cubanetype [Mo3S4]4+ clusters,60 and MoIV-disulfide complexes,61 with
slightly varying Mo−S bonding structures.
The Tafel Slopes measured from multiple samples are in the
range of 105−120 mV/dec (Supporting Information, Table
S10), which suggests that the rate-determining step in the HER
mechanism on our MoS2 and MoSe2 catalyst is the Volmer
reaction,62,63 a discharge step that converts protons into
absorbed hydrogen atoms on the catalyst surface. Previous
studies on MoS2 catalyst has shown a large spread of Tafel
slopes ranging from 40 mV to 120 mV/dec.38,41,42,50,59,64 Tafel
slopes observed here are on the larger side of this range. A small
Tafel slope is desired for practical application of HER catalysts,
and the overall perfomance of edge-terminated MoS2 and
MoSe2 films should be further improved. Our preliminary study
suggests the slow discharge reaction can be partially accelerated
by tuning the substrate morphology and the choice of the
material. The edge-terminated MoS2 film prepared on rough,
lapped glassy carbon substrate exhibits a Tafel slope of 86 mV/
dec (Supporting Information, Figure S7), whereas edgeterminated MoS2 film on Mo foil shows a Tafel slope of 75
mV/dec (Supporting Information, Figure S8). The improvements suggest viable avenues to optimize the overall kinect
current density of edge-terminated MoS2 and MoSe2 catalysts.
Stability is another important aspect for electrocatalysts. It is
a practical concern for edge-terminated, metastable MoS2 and
MoSe2 films studied here. The long-term stability is assessed by
taking continuous cyclic voltammograms in the cathodic
potential window at an accelarated scanning rate of 50 mV/
s.42,50 We set the lower potential limits (about −0.4 V for MoS2
and −0.45 V for MoSe2) to drive a very large cathodic current
density of 8 mA/cm2. The polarization curves before and after
cycling are recorded under quasi-equilibrium conditions with a
slower scan rate of 2 mV/s. Polarization curves after the 1000th
cycle almost overlay the curve of the first cycle with negligible
loss of cathodic current, as shown in Figure 6c and d. It
confirms that the edge-terminated films of MoS2 and MoSe2 are
stable in acidic electrolyte and remain intact through repeated
cycling. Notice that the current cutoff of 8 mA/cm2 is surfacearea-normalized kinetic current, and much higher geometric
Figure 6. Electrochemical measurements in a cathodic potential
window. (a) Polarization curves of edge-terminated MoS2 and MoSe2
films as well as a blank glassy carbon substrate showing H2 evolution.
(b) Corresponding Tafel plot (log current versus potential). Catalyst
stability tests for MoS2 (c) and MoSe2 (d) in which negligible HER
currents are lost after 1000 cycles in the cathodic potentials windows.
respectively. Notice that the current presented here is the
surface-area-normalized kinetic current, based on the specific
surface area acquired by AFM (Supporting Information, Table
S9). The exchange current density, j0, is determined by fitting
the linear portion of Tafel plot at low cathodic current to the
Tafel equation,38,57 yielding averaged values of 2.2 × 10−6 A/
cm2 for MoS2 and 2.0 × 10−6 A/cm2 for MoSe2 (Supporting
Information, Table S10). The structural characterization based
on TEM studies allow us to calculate edge site density and to
directly correlate the activity to each edge site, yielding a turn
over frequency (TOF) at 0 V of 0.013 s−1 for MoS2 and 0.014
s−1 for MoSe2 (Table 1). The TOF of MoS2 is very close to the
reported value of 0.016 s−1 obtained from combined STM
studies and in situ electrochemical measurements on MoS2
nanoplatelet catalysts.38 The close agreement of TOFs between
our ex situ measurements on edge-terminated MoS2 films and
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Figure 7. The effect of edges on HER activity studied by thermal annealing of the as-grown films. (a) STEM image of a MoS2 film, annealed at 550
°C for 2 h, retaining edge-terminated surface. (b) STEM image of a MoS2 film, annealed at 800 °C for 8 h, with multiple moiré fringes due to the
formation of randomly oriented particles. Low-magnification STEM image (inset) reveals the film is composed of plate-like particles on the order of
tens of nanometers. (c) Raman spectra from the as-grown and 800 °C-annealed MoS2 films show E12g mode with increased intensity, as well as
reduced peak widths and higher crystal quality upon annealing. (d) Tafel plot of the corresponding electrochemical measurements.
∼0.1 Å/s. Substrates are placed at the hot center of the tube
furnace. Sulfur/selenium powder (from Sigma Aldrich) is
placed at the upstream side of the furnace at carefully adjusted
locations to set the temperature. The tube is pumped to a base
pressure of 100 mTorr and flushed with Ar gas to remove
residue oxygen. Subsequently, the heating center of the furnace
is quickly raised to reaction temperature of 550 °C in 20 min,
and the sulfur/selenium precursor is kept at ∼220 °C and ∼300
°C respectively, well above their melting temperatures. The
furnace is held at reaction temperature for 10 min, followed by
natural cool-down, during which Ar gas is kept flowing at a rate
of 100 s.c.c.m. to transport sulfur/selenium to the substrate.
After the reaction, the mass loading is ∼8.5 μg/cm2 for MoS2
and ∼13.5 μg/cm2 for MoSe2.
Thermal annealing of MoS2 films are performed in the same
setup. During the process, sulfur vapor is supplied in the
furnace, to prevent the gradual depletion of sulfur in the film.
MoS2 single crystal is obtained from SPI Supplies to establish
a reference Raman spectrum of the terrace-terminated surface.
A fresh terrace-terminated surface is created by cleaving the
crystal using Scotch tape.
Characterizations. Characterizations were carried out using
TEM (FEI Tecnai G2 F20 X-Twin microscope at 200 keV and
aberration-corrected FEI 80-300 environmental Titan (S)TEM
microscope at 300 keV), Raman spectroscopy (WITEC Raman
spectrometer), X-ray photoelectron spectroscopy (XPS, SSI SProbe XPS spectrometer with Al(Ka) source), atomic force
microcopy (AFM, Park Systems XE-70), and scanning electron
microscopy (SEM, FEI Nova NanoSEM 450). Films for TEM
characterization are prepared on an oxidized silicon substrate
(300 nm SiO2/Si), followed by a lift-off process to transfer the
films onto carbon membranes supported on nickel TEM grids
by etching away the sacrificial SiO2 layer with dilute HF
solution. For electron tomography, the sample was tilted to
±64° while taking aberration-corrected TEM images at 1° tilt
increments. Gold particles were used to decorate the sample as
fiducial markers for postalignment of the tilt series. A weighted
back-projection was used to reconstruct the three-dimensional
data. Volume-rendering in Amira was used to visualize the
reconstructed data. In Figure 1d, the top surface of the
reconstruction is replaced with a cross-section of the tomogram
to enhance the contrast for clearly visualizing individual layers.
Supplementary Movies S11 and S12 show the original
reconstructed tomogram of MoS2 film in different perspectives.
kinetic current can potentially be achieved if the films are
grown on high surface area substrates.
As the edge-terminated films are a kinetically synthesized
product, we attempted to reduce the number of edge sites on
the films by annealing, to correlate the edge site density to the
catalytic activity. Figure 7a and b present dark field scanning
transmission electron microscopy (STEM) images of edgeterminated MoS2 films annealed at 550 °C for 2h and at 800 °C
for 8h, respectively. Annealing at the synthesis temperature of
550 °C does not affect the texture of the film. To reduce the
high-energy edge surface, multiple grains should rotate and
migrate simultaneously, which imposes a large energy barrier to
overcome. Accordingly, our edge-terminated films represent a
metastable form of molybdenum chalcogenides. After annealing
at 800 °C for an extended period, the film converts into
particulate morphology with randomly oriented platelet-like
nanoparticles with dimension of tens of nanometers. The
growth of these nanoparticles reduces the number of edge sites,
which is driven by the tendency to decrease the overall surface
energy. In Figure 7c, the relative intensities of Raman modes
from 800 °C annealed film lie between the terrace-terminated
and edge-terminated films, since the preferential orientation of
the layers is lost. The annealed MoS2 film also exhibits
improved crystalline quality, evidenced by the reduction of peak
widths in the Raman spectrum. Corresponding electrochemical
measurements in Figure 7d indeed show decreased HER
activity for the 800 °C annealed film, with much lower
exchange current density than as-grown samples. This confirms
that the number of edge sites is critical for catalytic activity,
whereas the crystalline quality is less important.
The chalcogenide films with high-density edge sites
represents a novel metastable structure of layered materials.
The unique structure paves the way to use the edges of layered
materials more effectively. In particular, the edge-terminated
layered chalcogenide films may have broad applications in
many important catalytic reactions, including hydrodesulfurization for the petroleum industry,35 oxygen reduction reactions
for fuel cells,39 and HER studied here.
Methods. Synthesis and Preparation. Edge-terminated
MoS2 and MoSe2 films are grown inside a single-zone, 12-in.
horizontal tube furnace (Lindberg/Blue M) equipped with a 1in.-diameter quartz tube. The synthesis setup is illustrated in
Figure 2a. The substrates are coated with 5-nm-thick Mo film as
a precursor by e-beam evaporation at a low deposition rate of
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Electrochemical Studies. MoS2/MoSe2 films are grown on
mirror polished glassy carbon (from HTW HochtemperaturWerkstoffe GmbH) to measure HER activities. Electrochemically inert, hydrophobic wax (Apiezon wax W-W100) is used to
define the 1 cm2 electrode area. A metal alligator clip is used to
connect the working electrode with an external circuit. The
measurements are performed in 0.5 M H2SO4 solution
(deaerated by N2) using a three electrode setup, with a
K2SO4 saturated Hg/HgSO4 reference electrode (from AMEL
instruments), a graphite rod (99.999%, from Sigma Aldrich)
counter electrode, and the glassy carbon working electrode.
The reference electrode is calibrated in H2 saturated electrolyte
with respect to an in situ reverse hydrogen electrode (RHE), by
using two platinum wires as working and counter electrodes,
which yields the relation E(RHE) = E(Hg/HgSO4) + 0.735 V.
The saturation condition is confirmed by minimizing the
potential difference between the working and counter electrodes to less than a few mV. Linear sweep voltammetry (scan rate
2 mV/s) and AC impedance spectroscopy (at zero overpotential) are recorded by a Biologic VSP potentiostat. For a
Tafel plot, the linear portion at low overpotential, corresponding to cathodic current density of less than 1 mV/cm2, is fit to
the Tafel equation. Within the low overpotential range, the fit is
not affected by the evolution of hydrogen bubbles or other
kinetic effects. All data have been corrected for a small ohmic
drop (<4 Ω) based on impedance spectroscopy.
■
ASSOCIATED CONTENT
S Supporting Information
*
Additional details on sample preparations, chracterizations,
electrochemical measurements, and analyses. This material is
available free of charge via the Internet at http://pubs.acs.org.
■
AUTHOR INFORMATION
Corresponding Author
*E-mail: yicui@stanford.edu.
Notes
The authors declare no competing financial interest.
ACKNOWLEDGMENTS
We acknowledge support by the Department of Energy, Office
of Basic Energy Sciences, Materials Sciences and Engineering
Division, under contract DE-AC02-76-SFO0515. We thank
Peter A. Ercius at National Center for Electron Microscopy,
Lawrence Berkeley National Laboratory for his tomography
reconstruction scripts. Author contributions are as follows: D.K.
and Y.C. conceived the experiments. D.K. and H.W.
synthesized and prepared the materials. J.J.C. carried out the
TEM characterization and electron tomography reconstruction.
D.K., H.W., J.J.C., K.J.K., and J. Y. performed additional
characterizations. M.P., D.K., and H.W. performed electrochemical measurements and analyses. All authors contributed
to scientific planning and discussions.
■
■
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