Hierarchical CoNiSe nano-architecture as a high ... · Hierarchical CoNiSe 2 nano-architecture as a...
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Hierarchical CoNiSe2 nano-architecture as a high- performance electrocatalyst for water splitting
Tao Chen and Yiwei Tan ()
State Key Laboratory of Materials-Oriented Chemical Engineering, School of Chemistry and Chemical Engineering, Nanjing Tech University, Nanjing 210009, China
Received: 10 May 2017
Revised: 11 June 2017
Accepted: 23 June 2017
© Tsinghua University Press
and Springer-Verlag GmbH
Germany 2017
KEYWORDS
bifunctional catalysts,
electrocatalysis,
nanostructures,
ternary selenide,
water splitting
ABSTRACT
Hierarchical nano-architectures comprised of ultrathin ternary selenide (CoNiSe2)
nanorods were directly grown on nickel foam (NF). The integrated CoNiSe2/NF
functions as a robust electrocatalyst with an extremely high activity and stability
for emerging renewable energy technologies, and electrochemical oxygen and
hydrogen evolution reactions (OER and HER, respectively). The overpotentials
required to deliver a current density of 100 mA·cm−2 are as low as 307 and 170 mV
for the OER and HER, respectively; therefore, the obtained CoNiSe2 is among
the most promising earth-abundant catalysts for water splitting. Furthermore,
our synthetic sample validates a two-electrode electrolyzer for reducing the cell
voltage in the full water splitting reaction to 1.591 V to achieve a current density
of 10 mA·cm−2, which offers a novel, inexpensive, integrated selenide/NF electrode
for electrocatalytic applications.
1 Introduction
Electrochemically converting water to H2 and O2 is a
promising strategy for developing clean, renewable
energy sources [1–3], and is greatly dependent on the
rational design of highly active, stable, and cost-effective
hydrogen- and oxygen-evolving catalysts. Water splitting
via an electrochemical route requires extremely large
overpotentials closely related to the coupled four-
electron and four-proton transfer processes with high
activation barriers [4], which is rather intractable.
Platinum-group metals and metal oxides are the most
efficient catalysts in this respect, but they are scarce
and expensive. Therefore, there has been intense
research into highly active, commercially viable
electrocatalysts based on earth-abundant elements
to overcome these challenges. Concomitantly, new
inspirations are expected to be acquired for developing
higher levels of catalytically active centers.
Recently, the design of inexpensive water splitting
electrocatalysts was achieved by optimizing the com-
position of nonprecious metal catalysts and fabricating
sophisticated nano-architectures, which provide a
large surface area, more active sites, and/or robust
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https://doi.org/10.1007/s12274-017-1748-3
Address correspondence to [email protected]
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1332 Nano Res. 2018, 11(3): 1331–1344
structures for improving the activity and long-term
durability of the catalysts. In this respect, most
research has been targeted toward the synthesis and
modulation of nanostructured 3d transition metal
(3d-TM) chalcogenides [5–11], such as CoS [12], CoS2
[13], CoSe2 [14–21], Co(SxSe1−x)2 [22], CoSP [23], NiS2
[24], NiSe [25–27], Ni3S2 [28, 29], and Co(Fe)–Ni–S(Se)
[30–38], because they show higher activities and con-
ductivities than their oxide/hydroxide counterparts.
In contrast to binary 3d-TM chalcogenides and their
mixtures, ternary bimetallic chalcogenides, especially
bimetallic selenides [34–38], have rarely been inves-
tigated, while such nanostructured catalysts may be
optimized candidates because a greater number of
active sites and synergistic effects (typically, improved
d-band states of the bimetallic active centers) are
provided by different metal constituents. This gap
is largely due to a lack of synthetic methods for
engineering the nano-architecture of bimetal-based
chalcogenides.
To develop more active electrocatalysts with complex
compositions, such as the Co(Fe)–Ni–S(Se) systems,
stepwise synthetic procedures were generally adopted
by using nanostructured bimetallic oxides/hydroxides
as the templating precursors [29–36]. Compared to
direct synthesis of multi-component chalcogenides,
the stepwise synthetic strategy often lacks flexible
and versatile control over the diverse morphologies
and architectures of the resulting products because
of the topotactic conversion reactions. CoSe2 and NiSe
nanostructures exhibit high activities toward the
hydrogen and oxygen evolution reactions (HER and
OER, respectively) [15–21, 25–27]. Therefore, the Co–
Ni–Se system, which contains highly active Co and
Ni centers, could conceivably be a fascinating
electrocatalyst for the HER, OER, or both. However, a
pure compound of the ternary Co–Ni–Se system has
rarely been studied as a bifunctional electrocatalyst
for both the HER and OER, even though doped
systems and a two-phase mixture have been reported
in the literature [36–38]. Herein, we describe a simple
method for one-step growth of the hierarchical ternary
CoNiSe2 nano-architecture on Ni foam (CoNiSe2/Ni),
which serves as an excellent bifunctional electrocatalyst
for both the OER and HER, using Ni foam as both
the Ni source and catalyst support to fulfill the high
activity and long-term stability demands. We also
grew NiSe nanosheets (NSs) directly on the Ni foam
(NiSe/Ni) as a control. Furthermore, in a two-electrode
water electrolyzer comprised of CoNiSe2/Ni, a
10-mA·cm−2 water-splitting current is achieved at a cell
voltage of 1.591 V, which is superior to that provided
by most of the earth-abundant 3d-TM chalcogenide-
and phosphide-based electrolyzers reported to date.
2 Experimental
2.1 Chemicals
Selenic acid (Alfa Aesar, H2SeO4, 40% aqueous solution),
2-methoxy-5-nitroaniline (MNA, Alfa Aesar, > 98%),
cobalt(III) acetylacetonate (Co(acac)3, Sigma-Aldrich,
> 98%), nickel foam (1.5-mm thickness, Ailantian
Advanced Technology Materials Co. Ltd.), Pt/C
(Johnson Matthey, 20 wt.% of 3.2-nm Pt nanoparticles
(NPs) on a Vulcan XC-72 carbon support), pyridine
(Sinopharm Chemical Reagent Co., Ltd. (SCRL), 99%),
N-methyl-2-pyrrolidinone (Alfa Aesar, 99%), and
anhydrous ethanol (SCRL, 99.5%) were used without
further purification. All water used in this work was
purified using a Millipore Milli-Q system (resistivity
> 18.0 MΩ·cm−1).
2.2 Synthesis of the electrocatalysts
2.2.1 Synthesis of a hierarchical CoNiSe2 nano-architecture
on Ni foam
A piece of Ni foam was cut into equal parts (1 cm × 3 cm)
and sequentially pretreated with acetone, hydrochloric
acid (0.1 M), and ethanol under ultrasonication to
remove grease and the surface oxide layer. MNA
(121.1 mg) and Co(acac)3 (85.6 mg) were dissolved
in a mixed solvent of pyridine (20 mL) and water
(11.5 mL), and then mixed with 6 mL of an aqueous
solution of selenic acid (0.08 M) (Co/Se molar ratio of
1:2). Then, the reaction solution was transferred to a
40-mL Teflon-lined autoclave. The cleaned and dried
Ni foam was immersed into the autoclave. The autoclave
was sealed and maintained at 180 °C for 24 h and
then naturally cooled to ambient temperature. The
resulting Ni foam covered with CoNiSe2 (CoNiSe2/Ni)
was removed, washed 5 times with ethanol and
N-methyl-2-pyrrolidinone at 50 °C, and dried.
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2.2.2 Synthesis of NiSe2 nanosheets on Ni foam
MNA (121.1 mg) was dissolved in 31.5 mL of pyridine;
then, it was mixed with 6 mL of an aqueous solution
of selenic acid (0.08 M) under vigorous ultrasonication.
Next, the reaction solution was transferred to a
40-mL Teflon-lined autoclave, and the cleaned Ni
foam (1 × 3 cm2) was immersed into the reaction
solution. The autoclave was sealed and maintained at
180 °C for 20 h and then naturally cooled to ambient
temperature. Finally, the resulting Ni foam with
the product (NiSe/Ni) was cleaned according to the
procedure described in section 2.2.1.
2.3 Electrochemical measurements
All electrochemical measurements were performed
using a CHI 660D electrochemical analyzer (CH
Instruments, Inc.) in a standard three-electrode con-
figuration consisting of a well-cleaned CoNiSe2/Ni or
NiSe2/Ni working electrode, Ag/AgCl (KCl saturated)
reference electrode, and platinum wire counter
electrode in one compartment. Note that the effects of
the platinum wire on the OER and HER are negligible
[39, 40]. For comparison, RuO2 NPs prepared according
to a recent report [41] and Pt/C (20 wt.%) benchmarks
were loaded onto Ni foam using a Nafion solution
(5 wt.%) with the same catalyst loading as that of the
CoNiSe2/Ni electrode. The Ag/AgCl reference electrode
was calibrated with respect to the reversible hydrogen
potential using a platinum wire as both the working
and counter electrodes after each measurement. Linear
scan voltammetry (LSV) and cyclic voltammetry (CV)
curves were recorded in a supporting electrolyte (1 M
KOH) at a scan rate of 2 mV·s−1. Electrochemical
impedance spectroscopy (EIS) measurements were
performed by sampling 130 points in the frequency
range from 100 kHz to 0.01 Hz centered at −0.20 or
1.45 VRHE (RHE = reversible hydrogen electrode) for
the HER or OER, respectively, with an AC perturbation
of 5 mV. All plots for evaluating the electrocatalytic
activity toward the HER or OER were recorded after
continuous purging of H2 or O2 and were corrected
by a background capacitive current and ohmic potential
drop (iR) based on the series resistances derived from
EIS. For the overall water splitting test, two symmetric
catalyst electrodes were used as the anode and
cathode.
2.4 Characterization of materials
Scanning electron microscopy (SEM) was performed
using a Hitachi S-4800 field-emission scanning electron
microscope operating at 5 kV to investigate the
morphology of the catalysts. Transmission electron
microscopy (TEM) and high resolution TEM (HRTEM)
micrographs were acquired using an FEI Tecnai G2
F20 S-Twin transmission electron microscope operating
at an accelerating voltage of 200 kV. Scanning TEM
(STEM) micrographs and energy-dispersive X-ray
spectroscopy (EDS) elemental maps were obtained in
high-angle annular dark field (HAADF) mode using
the same transmission electron microscope. The
specimens for TEM observations were scratched from
the Ni foam substrate and sonicated before dropping
them onto 300 mesh carbon-coated copper grids. X-ray
photoelectron spectroscopy (XPS) measurements were
carried out using a PHI5000 VersaProbe (ULVAC-PHI)
spectrometer with an energy analyzer, employing a
monochromatized microfocused Al Kα (hv = 1,486.58 eV)
X-ray source. Samples for XPS measurements were
scratched from the Ni foam substrate and then
pretreated by repeated cycles of Ar+ ion sputtering to
obtain clean sample surfaces. The binding energies
(BEs) of the core levels were calibrated by setting the
adventitious C 1s peak at 284.8 eV. Survey spectra of
the samples in the BE range of 0–1,000 eV, and the core
level spectra of the elemental signals were recorded
at resolutions of 1 and 0.125 eV, respectively. The
X-ray diffraction (XRD) patterns were recorded using
a Rigaku SmartLab diffractometer with Cu Kα radiation
(λ = 1.5406 Å) operating at 40 kV and 100 mA at a
scanning rate of 0.06°·s−1. The monolithic Ni foam
covered with an as-grown catalyst was used as the
specimen for XRD analysis after a cleaning treatment.
The chemical composition of each sample was
determined by inductively coupled plasma atomic
emission spectrometry (ICP-AES, Prodigy, Leeman
Labs Inc., λ = 165–800 nm, As = 200 nm) after dissolving
the sample in aqua regia. The amount of O2 and H2
evolved under illumination was quantified using
gas chromatography (GC, Shimadzu, GC-8A) with a
thermal conductivity detector and Ar as the carrier
gas. The applied potential for the gas evolution
measurements was set at 1.63 VRHE in an airtight
two-electrode cell.
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3 Results and discussion
3.1 Hierarchical CoNiSe2 nano-architecture
Figure 1 shows the morphological and structural
features of the hierarchical CoNiSe2 nano-architecture
that was solvothermally grown on a piece of Ni foam
(designated as CoNiSe2/Ni hereafter). Figures 1(a)–1(c)
display top-view SEM images of CoNiSe2/Ni at
different magnifications. In contrast to the Ni foam
(see Fig. S1(a) in the Electronic Supplementary Material
(ESM)), the overview SEM image in Fig. 1(a) reveals
that the skeletal surface of the Ni foam is evenly
covered with dense, multilayered CoNiSe2 nanorods
(NRs) that grow radially from the substrate to form
hierarchical sea urchin-like microstructures, as evidenced
by the image of these NRs at a high magnification
(Fig. 1(b)). Further, many NRs align in a certain
direction and closely pack into clustered needle-like
bunches (Fig. 1(c)). Evidently, the diverse orientations
of the alignment of CoNiSe2 NRs provide omnidirec-
tional contact with the electrolyte and sufficient
interspace for electrolyte percolation and transfer,
favoring mass-transport. In addition, such a high-
density packing of NRs substantially boosts the
Figure 1 (a) Low-, (b) moderate-, and (c) high-magnification SEM images; (d) TEM and (e) HRTEM images; and (f) XRD pattern of the CoNiSe2 NRs directly grown on the Ni foam. The peaks labelled with asterisks in (f) originate from the Ni foam substrate. Forcomparison, the intensities and positions for the pure CoNiSe2 reference are given according to the JCPDS database (orange lines at the bottom of (f). Insets: (a) schematic illustration of the clustered CoNiSe2 NRs grown on Ni foam; (f) HAADF-STEM image and the corresponding EDS elemental mapping images of Co, Ni, and Se for CoNiSe2 NRs. Elemental mapping was performed in the area enclosed by a yellow box in the STEM image.
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structural robustness for electrocatalytic applications.
To clearly depict the CoNiSe2/Ni morphology, a
schematic of the hierarchical arrays of CoNiSe2/Ni is
shown in the inset of Fig. 1(a). The cross-sectional
SEM image shows the CoNiSe2 NRs with lengths up
to 0.5 μm (Fig. S1(b) in the ESM).
Figure 1(d) presents a representative TEM image of
several CoNiSe2 NRs with very uniform, thin diameters
of approximately 7 nm, together with some broken
NRs caused by scratching while preparing the TEM
specimens. The corresponding HRTEM image of these
NRs shows their single crystalline nature, evidenced
by the well-resolved, perfectly ordered lattice fringes
with an interplanar spacing of 2.72 Å, in accordance
with the value (2.72 Å) of the (101) planes of CoNiSe2
(Fig. 1(e)). The HAADF-STEM image and the corres-
ponding EDS elemental mapping images demonstrate
that Co, Ni, and Se are homogeneously distributed
over the entire NRs (see the insets in Fig. 1(f)). The
stoichiometry of the NRs (determined by EDS and
ICP-AES quantitative analyses; Table 1 and Fig. S2 in
the ESM) suggests the chemical identity of the NRs as
CoNiSe2. The XRD pattern in Fig. 1(f) also confirms
that the product is CoNiSe2 because the Bragg peaks
can be perfectly indexed to the hexagonal CoNiSe2
phase with lattice constants a = 3.646 Å and c = 5.337 Å
(JCPDF No. 65-7038), except for three strong peaks
stemming from the Ni substrate.
XPS was employed to further refine the composition
and chemical state of the CoNiSe2 NRs, as shown in
Fig. 2. As expected, the XPS survey spectrum in Fig. 2(a)
shows the Co, Ni, and Se signals in addition to those
from oxides and adventitious C species. The Co 2p
core level spectrum reveals the presence of two spin-
orbit doublets at 781.6 and 796.1 eV, together with two
satellite peaks at 786.5 and 803.0 eV (Fig. 2(b)), which
are associated with the BEs of Co2+ and Co3+ at the
Table 1 Parameters for comparing the electrocatalysts
Electrocatalysts Bulk atomic ratio Co:Ni:Se
XPS atomic ratio Co:Ni:Se
Crystal structure
(hexagonal)
CoNiSe2 23.5:27.7:48.8a
24.1:25.6:50.3b 22.1:28.4:49.5 a = 3.646 Å
c = 5.337 Å
a Data determined by EDS quantitative analysis. b Data obtained from ICP-AES measurements.
surface of the CoNiSe2 NRs [14, 33]. Co3+ species form
because of the harsh solvothermal conditions. The
high-resolution spectrum in the Ni 2p region (Fig. 2(c))
exhibits two peaks at 855.5 and 873.3 eV assigned to
the BEs of Ni 2p3/2 and Ni 2p1/2, respectively [25, 33].
Concomitantly, the presence of two satellite peaks at
861.2 and 879.6 eV further confirms the formation of
Ni2+ ions at the surface of the CoNiSe2 NRs. The Se 3d
XPS spectrum in Fig. 2(d) shows the BE of the main
line that consists of a doublet at 54.2 (Se 3d5/2) and
55.1 eV (Se 3d3/2) and originates from the Se moiety of
CoNiSe2. Meanwhile, a peak centered at 60.0 eV and
a doublet obtained after deconvolution of the weak
hump can be attributed to selenium oxides from surface
oxidation and Co 3p peaks, respectively. Deconvolution
of the O 1s signal in Fig. 2(e) reveals that the peaks at
530.4, 531.2, 532.1, and 533.2 eV can be assigned to
the oxygen species that originate from metallic oxides,
hydroxyl groups, selenium oxides, and water, respec-
tively [36]. The XPS surface chemical composition
does not visibly differ from the bulk composition
(Table 1).
The above morphological, structural, and com-
positional analyses consistently suggest that hierarchical
CoNiSe2 NR arrays successfully grew on the Ni foam.
The growth mechanism for CoNiSe2/Ni is proposed
in the following. MNA plays an important role in
dictating the growth of the hierarchical CoNiSe2
nano-architecture. If the reaction had been performed
in the absence of MNA while keeping the other
experimental parameters the same, a monolithic
featureless film structure would have formed
(Fig. S3(a) in the ESM). MNA first functions as a
reducing agent that reduces selenic acid to elemental
Se; subsequently, ploy(MNA) forms after oxidative
polymerization and acts as a capping reagent for the
one-dimensional growth of the CoNiSe2 NRs in
virtue of the amine group (–NH–) ligand. Indeed,
HRTEM observations reveal that all the as-prepared
CoNiSe2 NRs that were not subjected to washing are
covered with a thin, compact polymer shell (Fig. S3(b)
in the ESM), which is indicative of a strong affinity
of ploy(MNA) for the surface of the CoNiSe2 NRs.
More importantly, the formation of such a CoNiSe2–
ploy(MNA) core–shell structure is extremely favorable
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1336 Nano Res. 2018, 11(3): 1331–1344
for protecting CoNiSe2 NRs against oxidation by
water–O2 molecules during growth. The MNA-assisted
synthetic route for preparing the integrated CoNiSe2/
Ni electrode is schematically depicted in Fig. 3. To
demonstrate the generality of our synthetic method
and the effects of composition on the catalytic activity,
ultrathin NiSe NSs directly grown on Ni foam
(designated as NiSe/Ni thereafter) were also prepared
using a similar procedure (see Figs. S4 and S5, and the
related discussion in the ESM). Note that the NiSe
NSs are integrated into flower-like architectures. The
mass loadings of the CoNiSe2 NRs and NiSe NSs
are 1.84 and 2.93 mg·cm−2, respectively, based on the
ICP-AES quantitative analysis.
3.2 Electrocatalysis of water splitting
Figure 4(a) illustrates the polarization curves of the
CoNiSe2/Ni, NiSe2/Ni, and RuO2 NPs by plotting
the geometrical current density against the applied
potential to compare the OER activity. Note that all
potentials are referenced to an RHE in the text. As
shown in previous reports [25, 36, 38], the oxidation
Figure 2 XPS spectra collected from the CoNiSe2 NRs scratched from the CoNiSe2/Ni electrode. (a) XPS survey spectrum, and (b) Co 2p,(c) Ni 2p, (d) Se 3d, and (e) O 1s detail spectra.
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Figure 3 Schematic illustration of the procedure for fabricating the CoNiSe2/Ni catalytic electrode. The reaction processes are: (i) nH2SeO4 + 4nMNAs → nSe + poly(MNA) ((4MNAs)n) + 4nH2O; (ii) nCo(III)(acac)3 + 4nMNAs → nCo(II)(acac)2 + poly(MNA) ((4MNAs)n) + nHacac; (iii) 5Se + 2Co(II) + 2Ni + 3H2O → 2CoNiSe2 + H2SeO3 + 4H+. The bottom panel shows a digital photograph comparing the pristine Ni foam and the converted product, i.e., a piece of a CoNiSe2/Ni electrode. The color of the surface of the Ni foam changes from silver-white to black, demonstrating successful growth of the CoNiSe2 NRs on the surface.
Figure 4 (a) Polarization curves, (b) Tafel plots, and (c) Nyquist plots of different electrodes. (d) Chronopotentiometric curve ofCoNiSe2/Ni recorded at a constant current density of 100 mA·cm−2. Insets: a closeup of the Nyquist plot of CoNiSe2/Ni (left) and the equivalent circuit used to model all the electrode systems (right).
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peaks in the range of 1.40–1.45 VRHE are assigned to the
oxidation of Ni and/or Co species. The CoNiSe2/Ni
electrode shows the highest activity with the lowest
onset potential and the highest current density. A
steep rise in current density that accompanies the
vigorous release of O2 bubbles from the CoNiSe2/Ni
anode surface is observed while the potential is scanned
toward a positive value (see Movie S1 in the ESM). In
contrast, the bare Ni foam exhibits no current below
1.55 VRHE and the smallest anodic current above 1.55
VRHE. The CoNiSe2/Ni, NiSe/Ni, and RuO2 anodes
deliver a current density of 100 mA·cm−2 at overpo-
tentials (ηOER) of 307, 350, and 374 mV, respectively.
Notably, the activity of CoNiSe2/Ni is superior to
the NiSe/Ni and RuO2 benchmark and to most
reported chalcogenides, with only the exception of
the NixFe1−xSe2–DO hybrid nanoplates reported
recently (see Table S1 in the ESM) [33].
The Tafel slopes for the CoNiSe2/Ni, NiSe/Ni, and
RuO2 NPs obtained after iR correction are 79, 94, and
116 mV·dec−1, respectively (Fig. 4(b)), which verify
the fastest OER kinetics on the surface of CoNiSe2/Ni
because it shows the smallest Tafel slope value.
Figure 4(c) shows the Nyquist plots of EIS from
modeling with a Randles circuit comprising a series
resistance (Rs), charge transfer resistance (Rct), and
constant phase element (the right inset in Fig. 4(c)).
The small Rs values (< 3 Ω) for CoNiSe2/Ni and NiSe/
Ni suggest their outstanding electric conductivity
and integrated architecture. In particular, the Rct of
CoNiSe2/Ni (~ 0.27 Ω) is much smaller than those of
the NiSe/Ni (2.28 Ω) and RuO2 NPs (3.21 Ω), further
demonstrating an insignificant Rct and the fastest
reaction rate on the CoNiSe2/Ni surface. The time-
dependent potential curve recorded at 100 mA·cm−2
for 20 h is used to assess the stability of CoNiSe2/Ni
for the OER (Fig. 4(d)). The long-term stability of the
CoNiSe2/Ni electrode for OER is confirmed by the
maintained potential round 1.54 VRHE over a period of
20 h. Note that the potential required for delivering
100 mA·cm−2 increases slightly from an initial value
of 1.537 to 1.546 VRHE after 20 h of operation. Further-
more, the stability of CoNiSe2/Ni can also be validated
from the nearly identical current density after 3,000
potential cycles of CV measurements for the OER
scan (Figure S6 in the ESM). The elevated intensity of
the redox peaks after 3,000 cycles can be attributed to
the increased concentration of Ni(III) species, e.g.,
NiOOH [30], in the “skin” of CoNiSe2/Ni after the CV
measurements. However, the XRD pattern of this
tested sample shows no XRD peaks arising from other
matters, implying a stable bulk phase of CoNiSe2
during the continuous electrolysis process (Fig. S7 in
the ESM). The SEM images exhibit a perfect retention
of the CoNiSe2 nano-architecture, even after 20 h of
OER (Fig. S8 in the ESM), suggesting an excellent
structural robustness of the electrode stemming from
the bound NRs. As expected, the corresponding XPS
spectra exhibit that the surface of the CoNiSe2 NRs is
enriched by oxidized Ni and Co species after OER
(Fig. S9 in the ESM), where the appearance of the
essential Ni(III) and Co3O4 catalytic species is critical
for promoting OER [25, 42]. Similarly, Ni(III) species
are also formed on the surface of the NiSe NSs
(Fig. S10 in the ESM). Concomitantly, the surface
coverage of SeOx for both samples is increased because
the XPS peak of the metal–Se moiety disappears
(Figs. S9 and S10 in the ESM). Clearly, our CoNiSe2
NRs and NiSe NSs provide both catalytically active
surface species for the OER and a highly conductive
backbone for electron transport.
Figure 5(a) compares the capacitance- and
iR-corrected polarization curves of CoNiSe2/Ni, NiSe/Ni,
and Pt/C for testing the activity toward the HER. The
CoNiSe2/Ni and NiSe/Ni electrodes exhibit very high
electrocatalytic activities toward HER with onset
overpotentials of 42 and 56 mV, while their activities
are still slightly lower than that of the 20 wt.% Pt/C
that only needs a slight overpotential to induce an
onset current. Similar to the observations in a previous
study [25], the bare Ni shows a moderate HER
electroactivity and requires an overpotential of 262 mV
to deliver 10 mA·cm−2. In contrast, CoNiSe2/Ni requires
overpotentials of 87 and 146 mV to afford 10 and
100 mA·cm−2, respectively, and NiSe/Ni requires 171
and 239 mV to drive 10 and 100 mA·cm−2, respectively,
which clearly implies that the loaded CoNiSe2 and
NiSe nano-architectures offer the dominant electroac-
tivity to obtain a high throughput of H2 with a
relatively low overpotential. By comparing the onset
overpotential and the overpotential for marked H2
evolution as well as the catalyst loading with the
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1339 Nano Res. 2018, 11(3): 1331–1344
overpotentials for the 3d-TM chalcogenides reported
previously, our CoNiSe2/Ni catalyst ranks among the
best non-precious metal HER catalysts (Table S2 in
the ESM).
Figure 5(b) shows Tafel slopes of 40, 72, and
29 mV·dec−1 for CoNiSe2/Ni, NiSe/Ni, and Pt/C, res-
pectively. The small Tafel slope within the low potential
region for CoNiSe2/Ni, from which the exchange
current density (J0, geometrical) is estimated to be
0.37 mA·cm−2 based on the intercept of the Tafel plot,
indicates that the HER follows the Volmer–Heyrovsky
mechanism [30, 31]. This J0, geometrical value is lower
than that of NiSe/Ni (0.69 mA·cm−2) but is two orders
of magnitude higher than those for binary CoS2 and
CoSe2 [14, 15]. Concomitantly, the Nyquist plots fitted
by the above Randles circuit reveal the faster reaction
rate for CoNiSe2/Ni, which is derived from its smaller
semicircle arc (Rct of 2.1 Ω) than that of NiSe/Ni (3.5 Ω)
(Fig. 5(c)). The performance stability of the CoNiSe2/Ni
electrode for HER is determined by the chronopoten-
tiometric curve, as shown in Fig. 5(d). The potential
required to deliver 100 mA·cm−2 varies from the initial
0.170 to 0.178 VRHE over 20 h of continuous electrolysis.
Such an insignificant increase in overpotential suggests
the excellent stability of the CoNiSe2/Ni for HER.
CV tests show a slight current degradation, further
verifying the excellent long-term durability (Fig. S11(a)
in the ESM). As for the OER, the morphology and
bulk crystalline structure of the CoNiSe2/Ni sample
that was subjected to continuous HER operation over
20 h remains unchanged (for brevity, the data are
not presented again). The corresponding Co 2p XPS
spectrum exhibits that the Co 2p3/2 and Co 2p1/2 lines
shift to lower BEs (778.6 and 793.9 eV, respectively),
suggesting the formation of Co2+ by cathodic reduction
[14, 16], while the Ni chemical state remains nearly
unchanged (Fig. 2 and Fig. S9 in the ESM). No per-
ceptible changes are observed in the Ni state for the
NiSe NSs after the HER (Fig. S10 in the ESM). The
XPS spectra reveal the increased content of SeOx after
the HER for both samples, while trace amounts of the
metal–Se moiety are still observed. The increase in
Figure 5 (a) Polarization curves, (b) Tafel plots, and (c) Nyquist plots of different electrodes. (d) Chronopotentiometric curve ofCoNiSe2/Ni recorded at a constant current density of 100 mA·cm−2.
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1340 Nano Res. 2018, 11(3): 1331–1344
the coverage of SeOx species is probably attributed
to the adsorption and reaction of O2 produced and
diffused from the anode with Se anions in alkaline
solution. For both post-OER and post-HER, the con-
version of the most metal–Se moiety into SeOx might
be favorable for the adsorption of H2O, therefore
leading to an enhanced water splitting rate.
The double-layer capacitances (Cdl) of the CoNiSe2/Ni
and NiSe/Ni electrodes are 9.3 and 25.9 mF·cm−2,
respectively, based on the scan rate dependence of the
charging current density (Fig. 6), where the slope of
the ΔJ vs. scan rate plot is twice Cdl. Thus, CoNiSe2/Ni
has a smaller electrochemically active surface area
(ECSA) than NiSe/Ni because the NRs are bound
together in bundles and have a lower loading. In the
case of the HER, the normalized exchange current
(J0, normalized) of CoNiSe2/Ni is 1.49 times larger than
that of NiSe/Ni based on the relative ECSA values.
Concomitantly, the turnover frequencies are 0.082 and
0.0056 H2 s‒1 for CoNiSe2/Ni and NiSe/Ni, respectively,
at an overpotential of 0.1 V, according to the method
given in the literature (Fig. S12 and the related dis-
cussion in the ESM) [43]. These results suggest
that the enhanced activity of CoNiSe2/Ni relative to
NiSe/Ni for HER may be associated with its ternary
composition. The previous theoretical investigations
proposed that the variations in electronic structure
contribute to the enhanced water splitting performance
for the ternary compounds [23, 30]; however, until
now, no direct experimental data have been available to
support such a notion. We thus compare the valence
band (VB) structures of the CoNiSe2 NRs and NiSe
NSs to effectively reinforce the modification of the
electronic structure (Fig. 8). According to the d-band
center (d-BC) position of each catalyst, which is
derived from the weighted average energy of the VB
Figure 6 Cyclic voltammograms of (a) CoNiSe2/Ni and (b) NiSe/Ni electrodes, which are used to estimate the double layer capacitances(Cdl). Scan rates from 2, 5, 10, 20, 50, and 100 to 200 mV·s−1 were chosen. (c) The capacitance currents vs. scan rate for the CoNiSe2/Ni and NiSe/Ni electrodes. The current value Δj was obtained by adding the absolute values of the anodic and cathodic currents at thecorresponding intermediate applied potential (0.30 and 0.10 VRHE for CoNiSe2/Ni and NiSe/Ni, respectively). The potential window for CoNiSe2/Ni is chosen at the more positive region to avoid the larger cathodic current that could result from the reduction of the surfaceCo(III) species (i.e., E
oCo(OH)3/Co(OH)2 = 0.17 V vs. normal hydrogen electrode).
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1341 Nano Res. 2018, 11(3): 1331–1344
Figure 7 XPS valence band spectra collected for the CoNiSe2 NRs (red curve), NiSe NSs (blue curve), CoSe2 nanoneedles (olive curve), and the mixture of CoSe2 and NiSe2 nanowires (black curve). A Shirley background is subtracted from each spectrum to eliminate the spectral background that originates from inelastically scattered electrons.
spectrum by subtracting the Shirley background and
integration, the d-BC energy (2.14 eV) of the CoNiSe2
NRs is lower than those of the NiSe NSs (3.24 eV),
CoSe2 nanoneedles (2.96 eV), and bi-phase mixture of
CoSe2 and NiSe2 nanowires (3.05 eV) (the latter two
controls were prepared by following the published
procedures as described in Refs. [19, 37], respectively).
Perceivably, charge transfer from Co to Ni (or vice
versa) is responsible for the change in the d-BC
energy. The diminution of the average energy of the
d electrons in CoNiSe2 weakens the chemisorption
energy of the intermediates (Had, OHad, and Oad) of
water splitting, which enables a low activation barrier
for the elementary reaction steps. Additionally, the
different morphologies for both samples could contribute
to the changes in the electronic structure and thus
provide another pronounced factor that influences
the water-splitting performance.
Considering that both CoNiSe2/Ni and NiSe/Ni
function as bifunctional electrocatalysts, a single
electrolyzer is constructed for overall water splitting
using a symmetric two-electrode setup consisting of
CoNiSe2/Ni or NiSe/Ni acting as both an anode and
cathode (designated as CoNiSe2/Ni||CoNiSe2/Ni or
NiSe/Ni||NiSe/Ni, respectively). A control RuO2||Pt/C
benchmark is also tested for comparison. Figure 8(a)
shows that a cell voltage of 1.59, 1.64, 1.56, or 1.91 V
is required to deliver a current density of 10 mA·cm−2
for the CoNiSe2/Ni||CoNiSe2/Ni, NiSe/Ni||NiSe/Ni,
RuO2||Pt/C, or blank Ni||Ni-based electrolyzer,
respectively. The CoNiSe2/Ni||CoNiSe2/Ni setup
outperforms or is comparable to other chalcogenide-
and phosphide-based electrolyzers (Table S3 in the
ESM), although this voltage is still lower than that for
the RuO2||Pt/C benchmark. The outstanding bifunc-
tionality endows CoNiSe2/Ni||CoNiSe2/Ni with a well-
improved overall water-splitting activity, albeit the
catalytic activity of single CoNiSe2/Ni toward HER or
OER is not supreme. The catalytic capability of the
CoNiSe2/Ni||CoNiSe2/Ni setup is evidenced by the
pronounced and vigorous H2 and O2 bubbles observed
on the electrodes at 10 and 180 mA·cm−2, respectively
(see Movies S2 and S3 in the ESM, respectively).
The long-term stability of CoNiSe2/Ni||CoNiSe2/Ni is
shown by the chronopotentiometric curve (Fig. 8(b)).
To preserve a current density of 10 mA·cm−2, a slightly
lower voltage at the initial stage and a nearly constant
voltage around 1.60 V is observed during the 20-h
operation. The faradic efficiencies (FEs) for the OER
and HER were obtained by comparing the H2 and O2
production quantified by GC with the calculated
amount according to the passed charge (Fig. 8(c)).
An FE of 100% for both the OER and HER is clearly
visible. Concomitantly, the ratio of O2 and H2 is close
to 1:2.
4 Conclusions
In conclusion, a simple and facile one-pot fabrication
process was developed to achieve a new, cost-effective
nanostructured ternary selenide (hierarchical CoNiSe2
NR arrays) supported on Ni foam, which serves as a
robust high-performance catalyst for electrochemical
water splitting. Compared to most 3d-TM chalcogenides
reported to date, our CoNiSe2/Ni electrode shows the
lowest overpotentials for delivering the same current
in the OER and HER, and a long-term durability. We
further demonstrate that an electrolyzer consisting of
CoNiSe2/Ni||CoNiSe2/Ni needs a remarkably low
cell voltage of 1.591 V to afford a current density of
10 mA·cm−2, which is among the best earth-abundant
3d-TM chalcogenide- and phosphide-based electrolyzers
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1342 Nano Res. 2018, 11(3): 1331–1344
reported thus far. Additional experimental results
reveal that the electronic structure of the ternary
CoNiSe2 NRs changes with respect to the mixture of
monometallic CoSe2 and NiSe2, which is one of the
factors accounting for the improved activity toward
HRE caused by the bimetallic component. Our studies
pave new ways for designing and innovating nano-
architectures of multicomponent 3d-TM compounds
as inexpensive, highly efficient, and versatile catalysts
for clean fuel generation.
Acknowledgements
This work was financially supported by the National
Natural Science Foundation of China (NSFC) (No.
21371097) and the Key University Science Research
Project of Jiangsu Province (No. 16KJA150004).
Electronic Supplementary Material: Supplementary
material (additional characterization results and
electrochemical data for this article) is available in
the online version of this article at https://doi.org/
10.1007/s12274-017-1748-3.
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