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Nano Res
1
Design of ZnO/ZnS/Au sandwich structure photoanode
for enhanced efficiency of photoelectrochemical water
splitting
Yichong Liu1, Yousong Gu1, Xiaoqin Yan1, Zhuo Kang1, Shengnan Lu1, Yihui Sun1, Yue Zhang1, 2 ()
Nano Res., Just Accepted Manuscript • DOI 10.1007/s12274-015-0794-y
http://www.thenanoresearch.com on April 17, 2015
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Nano Research
DOI 10.1007/s12274-015-0794-y
Design of ZnO/ZnS/Au Sandwich Structure Photoanode for
Enhanced efficiency of Photoelectrochemical Water Splitting
Design of ZnO/ZnS/Au Sandwich Structure
Photoanode for Enhanced efficiency of
Photoelectrochemical Water Splitting
Yichong Liu1, Yousong Gu1, Xiaoqin Yan1, Zhuo
Kang1, Shengnan Lu1, Yihui Sun1, Yue Zhang1 2
1. State Key Laboratory for Advanced Metals and
Materials, School of Materials Science and Engineering,
University of Science and Technology Beijing, China.
2. Key Laboratory of New Energy Materials and
Technologies, University of Science and Technology
Beijing, China.
We reported a sandwish structure for photoelectrochemical water
splitting photoanode enhanced by the introduction of ZnS interlayer
and Au nanoparticles
Design of ZnO/ZnS/Au Sandwich Structure Photoanode
for Enhanced efficiency of Photoelectrochemical Water
Splitting
Yichong Liu1, Yousong Gu1, Xiaoqin Yan1, Zhuo Kang1, Shengnan Lu1, Yihui Sun1, Yue Zhang1, 2 ()
Received: day month year
Revised: day month year
Accepted: day month year
(automatically inserted by
the publisher)
© Tsinghua University Press
and Springer-Verlag Berlin
Heidelberg 2014
KEYWORDS
ZnO, ZnS, Au,
photoanode,
photoelectrochemical
water splitting
ABSTRACT
We have demonstrated a ZnO/ZnS/Au composite photoanode with significantly
enhanced PEC performance with the ZnS interlayer and Au nanoparticles. The
solar-to-hydrogen conversion efficiency of such ZnO/ZnS/Au heterosturcture
reached 0.21%, which is 3.5 times that of pristine ZnO. The comparison of IPCE
and photoresponse in white and visible light region further verified that such
enhancement is attributed to the contribution of both UV and visible regions. The
modification of Au NPs can improve the PEC performance both in the UV and
visible regions due to the effective surface passivation and surface-plasmon-
resonance effects. And the ZnS interlayer is favorable for photogenerated
electrons under UV light and hot electron under visible light injection into ZnO,
simultaneously suppress the recombination at the photoanode-electrolyte
interface. The optimizing design of an interlayer between the plasmonic
metal/semiconductor composite systems reported here provides a facile and
compatible configuration to enhance the utilization efficiency of the incident light
for photoelectrochemical application.
1 Introduction Hydrogen that is formed by the solar splitting of water
is clearly considered to be the cleanest energy fuel to
meet future demand for energy, and various attempts
have been made in order to develop advanced
processes to produce hydrogen. Among these
different methods[1-3], photoelectrochemical (PEC)
water splitting, considered to be one of the most
promising hydrogen generation, is a highly-efficient
and eco-friendly way. In a PEC system, the selection
and design of the photoelectrode materials are critical
since the capability of the PEC cell for water splitting
is largely determined by the light absorption and
carrier transport of the photoelectrode. Light active
semiconductors or metal oxides such as titanium
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2 Nano Res.
dioxide (TiO2), Zinc oxide (ZnO), hematite (Fe2O3) and
cuprous oxide (Cu2O) have shown great potential for
hydrogen generation[4-13]. As a common and
inexpensive semiconductor, ZnO nanomaterials have
been extensively explored for solar energy conversion
because of their excellent electron mobility, electron-
transfer efficiency (115-155 cm2 V-1 s-1)[14], abundant
morphologies and favorable environmental
compatibility[15-18]. However, wide bandgap in ZnO
limits the photoelectrochemical (PEC) water splitting
performance due to poor absorption of visible light.
Therefore, it’s urgent to search for a strategy to
simultaneously increase the light capture.
Recently, plasmonic nanostructures of noble metal
especially gold (Au) have been demonstrated to be
promising for photocatalytic and solar energy
conversion due to its tunable interactions with light in
visible and infrared regions through a strong light
scattering and localized surface-plasmon resonance
(SPR) [19-22]. Also, Au nanoparticles are stable
enough for preventing corrosion during the
photoreaction[23]. Many efforts have been attempted
to design Au-ZnO based plasmonic nanostructures
for solar water splitting. The enhanced photoactivity
of Au NPs-decorated ZnO in the UV region is ascribed
to effective surface passivation as well as electric-field
amplification effect, while the photoactivity
enhancement in the visible region is mainly caused by
hot electron generation upon SPR excitation[24-28].
Therefore, it is highly desirable to design the ZnO/Au
photoanode for improving the efficiency of energy
conversion.
A suitable choice of interlayer material not only
reduces the recombination losses, but also enhances
the electron collection efficiency. The formation of ZnS
layer at the ZnO surface has been proved to be a
promising platform for photoelectrochemical water
splitting, due to fast photogenerated electron-hole
separation and enhanced injection efficiency[29-31].
The ZnO/ZnS/Au photoanode offers an optimal
configuration for PEC water splitting, as it
incorporates the merits of each composition.
In this paper, we demonstrated that the PEC
performance of ZnO/ZnS/Au photoanode can be
enhanced compared with pristine ZnO and ZnO/Au.
The PEC performance of different photoanodes were
systematically investigated with the illumination of
white light or visible light, respectively. The
ZnO/ZnS/Au sandwich structure possessed superior
photocurrent density compared with pristine ZnO
and ZnO/Au both in the UV and visible region, which
can be explained by EIS measurement and energy
band structure.
2 Experimental The fabrication sequence of ZnO/ZnS/Au nanorods
array via hydrothermal process[32], chemical
conversion process[33] and photochemical deposition
method[34] is shown in Scheme 1.
Scheme 1 Schematic Diagram of the Fabrication Procedure for
ZnO, ZnO/Au, and ZnO/ZnS/Au photoanodes
2.1 Synthesis of ZnO nanorods array. The samples
were prepared by the hydrothermal growth method.
A colloidal solution of zinc acetate [Zn(CH3COO)2
2H2O] (0.5 M) was spin-coated onto the FTO substrate
to form the ZnO seed layer, and subsequently
annealed at 350 °C in air for 30 min. In the
hydrothermal process, substrates were placed in the
aqueous solution containing 50 mM zinc nitrate
hexahydrate [Zn(NO3)2 6H2O] and
hexamethylenetetramine (HMTA) [(CH2)6N4] at 90 °C
for 12 h, with the seeded side facing down. Finally, the
substrate with product was repeatedly rinsed with
deionized water for several times and annealed in air
at 450 °C for 3h to remove residual surface salts.
2.2 Synthesis of ZnS interlayer. A simple chemical
conversion approach was adopted to fabricate
ZnO/ZnS core/shell nanostructures. The substrate
with ZnO nanorods array was immersed in
thiacetamide (TAA) aqueous solution (0.2 M) and the
sulfidation process was carried out at 95 °C for 15
minutes. The final product was also washed with
deionized water and ethanol repeatedly to remove the
impurities and dried at room temperature.
2.3 Synthesis of Au nanoparticles. The ZnO/ZnS and
ZnO nanorods array were immersed in a 10 ml
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3 Nano Res.
chloroauric acid (HAuCl4, 0.01%) solution with a
pH=7 adjusted by 0.1M NaOH solution, 1 ml 1%
polyvinyl alcohol ( PVA, [C2H4O]n ) and 0.5 ml
methanol (CH3OH, 99.5%). Under UV irradiation for
10 minutes, followed by calcination at 350℃ in N2 for
30 minutes, the Au ions (Au3+) were reduced to neutral
atoms attached to the surfaces.
2.4 Characterization of Materials. The structure and
morphology of the electrodes were characterized by
X-ray diffraction (XRD) (Rigaku DMAX-RB, CuKα),
field emission scanning electron microscopy (FE-SEM)
(FEI QUANTA 3D). The formation of ZnS and Au on
the ZnO nanorods and the bonding characteristics
were determined by X-ray photoelectron
spectroscopy (XPS, ESCALAB 250).
2.5 Eletrochemical Characterization. The photoanode
was fabricated by securing a copper wire on the
exposed electric conductive parts of the FTO with a
silver conducting paint. The substrate was
subsequently sealed on all edge with epoxy resin
except the active working area. All electrochemical
measurements were performed in a three electrode
mode with a photoanode as the working electrode, a
coiled Pt wire as counter electrode and a Ag/AgCl
reference electrode, and 0.5M Na2SO4 aqueous
solution (with pH buffered to ~7.0) as the electrolyte.
Electrochemical measurements were performed on an
electrochemical workstation (Solartron SI 1287/SI
1260). All photoanodes were illuminated from the
front side under AM 1.5G illumination provided by a
solar simulator (Oriel, 91159A). Visible light
illumination was obtained by passing the AM 1.5 light
through a 420 nm long-wave-passfilter. The white and
visible light intensity was 50 mW/cm2 and 45 mW/cm2
measured by a Si diode (Newport).
3 Results and discussion Figure 1(a) and (b) showed a typical SEM image of the
as-synthesized ZnO nanorods array with a smooth
surface. The side view (Figure 1(a)) clearly showed
that ZnO nanorods were aligned with a height of
about 5µm. The top view (Figure 1(b)) showed a dense
and oriented array of ZnO nanorods with the
diameter around 200 nm on the FTO substrate.
After sulfuration and Au-decoration, the morphology
changes of the nanorods array are observed in SEM
images. Figure 1(c) showed that Au nanoparticles
were uniformly distributed on the surface of each ZnO
nanorod and the nanorods still maintained their
vertically-oriented characteristics. The Au NPs
decoration of ZnO nanorods array was achieved by
the following reaction under UV illumination:
ZnO→ZnO(e+h)
ZnO(e+h)→e-+h+
AuCl4-+3e-→Au+4Cl-
As shown in Figure 1(d), different from the as-
synthesized ZnO/Au, the surface morphology after
the sulfuration became coarse, while the surface was
still hexagonal in shape and the nanorods were still
well-ordered, suggesting that sulfuration process did
not change the shape and size of the nanorods. During
the sulfuration, ZnO on the surface of nanowire was
etched and converted into ZnS, resulting in formation
of the ZnS shell:
CH3CSNH2+H2O=CH3CONH2+H2S
H2S=2H++S2-
ZnO+S2-+H2O=ZnS+2OH-
Figure 1 (a) Cross-sectional-view SEM images of the as-
synthesized ZnO nanorods array. Top view of pristine ZnO (b),
ZnO/Au(c) and ZnO/ZnS/Au (d) on an FTO substrate. (e) and (f)
TEM images of the ZnO/ZnS/Au.
The TEM image shown in Figure 1(e) (f) confirmed the
sandwich structure for ZnO/ZnS/Au. As can be seen,
the ZnS shell was uniform in width with the thickness
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4 Nano Res.
about 4 nm on the surface of ZnO nanorods, and the
surface-deposited Au nanoparticles had an average
diameter of 10~30 nm distributed on the surface of
ZnS. The composition of the as-prepared photoanodes
was further examined by energy-dispersive X-
ray(EDX) measurement, and the atomic ratios were
calculated from the EDX spectrum, as shown in Figure
S1 in the ESM.
XRD data of ZnO nanorods (blue curve in Fig. 2)
revealed that all diffraction peaks of the pristine
photoelectrodes were indexed to the planes of highly
crystalline ZnO (JCPDS file no. 36-1451) with no
impurities. Moreover, the main phase of all the
samples can be identified as the self-supported ZnO
nanoarchitectures with wurtzite (002) nanorods array,
which is consistent with SEM images. After the
decoration of Au nanoparticles, another two new XRD
peaks appeared at 2θ of 38.1° and 44.4°, which can be
identified as the characterisitic peaks of (111) and (200)
(JCPDS file no. 04-0784). For ZnO/ZnS/Au
photoanodes(red curve in Figure 2), a weak peak
belonging to ZnS (111) diffraction was detected at 2θ
~ 28.5°, resulting from a very thin ZnS layer coating on
ZnO (JCPDS file no. 05-0566).
Figure 2 XRD patterns of the ZnO, ZnO/Au and ZnO/ZnS/Au
photoanodes on the FTO substrate.
The XPS measurement of ZnO/ZnS/Au sample
demonstrated the presence of Zn, O, S and Au without
other unexpected elements (Fig. 3(a)). The high
resolution scans of Zn2p, S2p and Au peaks were
shown in Fig. 3(b), (c) and (d). The XPS data were
analyzed by fitting to a Gaussian−Lorentzian function
and using a Shirley background subtraction. The
Zn2p3/2 peak at 1021.8 eV and Zn2p1/2 peak at 1044.9
eV were shown in Fig. 3(b). In the S2p XPS spectrum
of Figure 3(c), the S2p3/2 and S2p1/2 peaks centered at
161.8 eV and 163.0 eV, respectively, are related to Zn−S
bondings, indicating that ZnS was successfully
synthesized by the chemical conversion process in our
experiments. XPS was further employed to identify
the chemical states of Au element. For Fig. 3(d), the
spectrum can be decomposed into two components,
which can be assigned to the peaks of Au04f7/2 and
Au04f5/2. It can be derived from the XPS results that the
Au constituent is in the metallic state.
Figure 3 XPS spectra of ZnO/ZnS/Au composite heterostructure:
(a) wide scan, (b) Zn2p, (c) S2p and (d) Au4f.
The PEC performance of various as-synthesized
different photoanodes were characterized through
photoinduced I-V curves. As can be seen, with the
introduction of ZnS interlayer, the ZnO/ZnS/Au
photoanode exhibited larger photocurrent density in
the whole potential window compared to ZnO/Au
and pristine ZnO photoanode. Under illumination as
shown in Figure 4(a), the photocurrent densities of the
prinstine ZnO, ZnO/Au and ZnO/ZnS/Au were 0.18
mA/cm2, 0.37 mA/cm2 and 0.58 mA/cm2 at 1V versus
Ag/AgCl. Sweeping the potential anodically, the I-V
curve of the ZnO/ZnS/Au exhibited a steeper increase
in current with respect to potential and achieved a
prompt saturation of the photocurrent density at 0.4 V
versus Ag/AgCl, suggesting much more efficient
charge separation and collection than in the prinstine
ZnO and ZnO/Au photoanode.
Furthermore, the photoconversion efficiencies (η) for
PEC water splitting of such photoanodes were
estimated using the following equation[35]:
η=I(1.23-Vapp)/Plight (1)
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5 Nano Res.
Vapp is the applied external potential versus reversible
hydrogen electrode (RHE). I is the externally
measured current density at Vapp. Plight is the power
density of the incident light. The potentials were
measured versus the Ag/AgCl reference electrode and
converted to the reversible hydrogen electrode (RHE)
scale using the Nernst function:
ERHE=EAg/AgCl+E°
Ag/AgCl+0.059pH (2)
ERHE is the converted potential versus RHE. EAg/AgCl is
the external potential measured against the Ag/AgCl
reference electrode. E°
Ag/AgCl is the standard electrode
potential of Ag/AgCl reference electrode (0.1976 V
versus RHE at 25 ℃). Figure 4(b) presented the plots
Figure 4 Comparisons of PEC properties of three different
photoanodes: prinstine ZnO (black), ZnO/Au (blue) and
ZnO/ZnS/Au (red): (a) Linear sweep voltammetry measurements
under simulated sunlight illumination with a 20 mV/s scan rate. (b)
Photoconversion efficiency as a function of applied potential
versus RHE.
of the photoconversion efficiencies vs RHE. The
ZnO/ZnS/Au exhibited an optimal photoconversion
efficiency of 0.21% at potential of 0.928 V vs RHE, 2
times and 3.5 times higher that of ZnO/Au (0.10% at
0.924 V vs RHE) and pristine ZnO (0.06% at 0.884 V vs
RHE) photoelectrode, respectively. The above
electrochemical results convincingly concluded that
the ZnS interlayer played positive roles in enhancing
the PEC water splitting efficiency of ZnO/Au
heterostructure.
For better revealing the influence of the ZnS interlayer
on the PEC performance of Au-ZnO based plasmonic
photoanode, chronoamperometic I-t curves were
collected at 0.5V vs Ag/AgCl with repetitive on/off
cycles under white light and visible light. As shown in
Figure 5 (a), the recorded photocurrent densities were
consistent with the values obtained from the linear
sweep voltammograms, indicating the photocurrents
are stable without photoinduced charging effect[36].
From the Diffuse reflectance UV−vis absorption
spectra, the absorption edge was extended to the
visible-light region due to the modification of Au NPs
(Figure S2 in the ESM). For visible light illumination,
the photocurrent density of ZnO /Au photoanode was
1.6 μA/cm2, while there was barely no photocurrent
for pristine ZnO photoanode. The enhanced
photocurrent in the visible region is caused by the SPR
effect of the modified Au NPs. With the introduction
of ZnS interlayer, the photocurrent density reached 3.9
μA/cm2, 1.6 times higher that of ZnO/Au photoanode,
demonstrating that the adjunction of ZnS layer could
enhance the visible-light photoactivity.
Furthermore, incident-photon-to-current-conversion
efficiency (IPCE) tests at 0.9 V versus RHE were
utilized to investigate the specific PEC active spectra
of as-systheised three different photoanodes. From
Figure 5(c), the ZnO/Au showed improved IPCE
values both in UV and VIS region due to Au NPs
modification. With the introduction of ZnS interlayer,
the IPCE values in the UV and VIS region were
improved compared to ZnO/Au photoanode, which
was consistent with its exclusive photocurrent
enhancement observed under white and visible light
illumination in Figure 5(a) and (b).
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6 Nano Res.
Figure 5 Chronoamperomertic I-t curves collected at 0.5V versus
Ag/AgCl for three different photoanodes under (a) white-light (50
mW/cm2) and (b) visible-light (45 mW/cm2). (c) IPCE curves for
three different photoanodes measured in the wavelength range
from 370 to 700 nm at an applied voltage of 0.9 V vs RHE.
Electrochemical impedance spectroscopy (EIS)
measurements were performed to further explore the
influence of the ZnS layer on the charge
recombination at an applied bias voltage of 0.1V vs
Ag/AgCl under white light and the results were fitted
by the equivant circuit in Figure 6. In the Figure 6, the
arch for ZnO/ZnS/Au photoanode was much smaller
than that of pristine ZnO and ZnO/Au photoanode,
implying that simultaneous introduction of the ZnS
and Au significantly reduced the resistance on the
movement of charge carriers at the interface. In this
work, the obtained results were fitted into the models
of a RC circuit inserted in Fig. 6. In this equivalent
circuit, Rs is the resistance of the device and Rct is the
interfacial charge-transfer resistance of the
photoanode-electrolyte interface. According to the
fitting data from the EIS results, the Rct were 3.93, 2.30
and 0.97 kΩ cm2 coupled for pristine ZnO, ZnO/Au
and ZnO/ZnS/Au photoanode, respectively. The Rct of
ZnO/Au was smaller than that of prinstine ZnO
indicated Au NPs enhanced the electron mobility by
surface passivation to reduce the recombination of
photoexcited electrons and holes[20]. With the
introduction of ZnS interlayer, surface traps states
such an oxygen vacancies /adsorb oxygen were
further reduced, resulting in the highest separation
efficiency of photogenerated electron-hole pairs and
fastest charge transfer of ZnO/ZnS/Au composite
structure[26]. Therefore, such results positively
supported the highest acquired water splitting
efficiency of ZnO/ZnS/Au in Figure 4(b).
Figure 6 (a) Nyquist plots measured at an applied potential 0.1 V
versus Ag/AgCl at white light for ZnO, ZnO/Au and ZnO/ZnS/Au,
respectively. The insert is a equivalent circuit employed to fit the
Nyquist plots.
For better understanding the electron-transfer
mechanism, we displayed the energy level diagram.
As illustrated in the Figure 7(b), surface plamons in
the Au NPs are photoexcited by visible light
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7 Nano Res.
illumination and hot electron-hole pairs are generated.
Subsequently, the hot electrons transiently occupying
Figure 7 Schematic for (a) the proposed mechanism of PEC water
splitting and (b) the energy band structure of the ZnO, ZnO/Au and
ZnO/ZnS/Au photoanodes.
the surface plasmon states (SP states) were transferred
to the conduction band of ZnO to improve
photocurrent in the visible region[25-26]. With the
introduction of ZnS in the Figure 7(c), the higher
conduction band position of the ZnS shell than ZnO
leads to faster electron transfer to conduction band[29].
And, when ZnO is stacked with ZnS, the lattice strain
existed along the interface of ZnO/ZnS
heterostructure can lead to an increase in the oscillator
strength, where the individual band gap could be
smaller than the initial value[37-39]. The band gap of
ZnO can be compressed resulting from the interface
strain from such a staggered II band alignment for
ZnO/ZnS heterostructure. From the point of view of
thermodynamic, the free energy change (ΔG) for the
plasmon-induced hot-electron transfer from the
surface plasmon resonance level to the CB of ZnS-
coated ZnO (ΔGtransfer) is more positive than that of
uncoated ZnO. As a result, the increased ΔGtransfer is
beneficial for electron transfer from excited Au to ZnO
via tunneling effect across a thin layer of ZnS, which
finally lead to the improved photocurrent density
with the introduction of ZnS layer under visible light.
4 Conclusions In summary, ZnO/ZnS/Au nanorods array have been
successfully fabricated to serve as the photoanode of
photoelectrochemical water splitting. The
photoconversion efficiency of the ZnO/ZnS/Au
photoanode reached to 0.21%, 2 times and 3.5 times
higher that of ZnO/Au and pristine ZnO photoanodes,
respectively. The ZnO/ZnS/Au sandwich structure
possessed superior photocurrent density compared
with pristine ZnO nanorods array photoanodes both
in the UV and visible region, which can be explained
by EIS measurement and energy band structure. The
surface passivation and surface-plasmon-resonance
effect of Au NPs can enhance the photocurrent under
illumination, while the introduction of ZnS interlayer
is favorable for electrons injection into ZnO and
reduces the recombination at the photoanode/
electrolyte interface. The optimizing design confirms
a new avenue of preparing efficient photoanode for
PEC water splitting.
Acknowledgements This work was supported by the National Major
Research Program of China (2013CB932601), the Major
Project of International Cooperation and Exchanges
(2012DFA50990), the Program of Introducing Talents of
Discipline to Universities(B14003), the National Natural
Science Foundation of China (51232001, 51172022,
51372023, 31371203), the Research Fund of Co-
construction Program from Beijing Municipal
Commission of Education, the Fundamental Research
Funds for the Central Universities, the Program for
Changjiang Scholars and Innovative Research Team in
University.
Electronic Supplementary Material: EDX and Diffuse
reflectance UV−vis absorption spectra is available in
the online version of this article at
http://dx.doi.org/10.1007/s12274-***-****-*. References
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