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Synthesis of FeS2 and Co-doped FeS2 films with the aid of supercriticalcarbon dioxide and their photoelectrochemical properties{
Jiqing Jiao, Liuping Chen,* Daibin Kuang, Wei Gao, Huajie Feng and Jian Xia
Received 18th April 2011, Accepted 26th April 2011
DOI: 10.1039/c1ra00066g
The prepared FeS2 and Co-doped FeS2 films revealed better properties in photocurrent response and
photocatalysis of water photolysis under simulated sunlight. The films were synthesized on iron
substrates with the aid of supercritical carbon dioxide. The experimental results demonstrated that
the supercritical carbon dioxide could play an important role in evolution of phases and
morphologies during the reaction process. Moreover, the prepared films were characterized by XRD,
SEM, TEM and EDS. The UV-vis absorption spectroscopy indicated that the absorption edge has
obvious blue shift compared with bulk FeS2. Interestingly, characteristics of photoelectric response
and water photolysis were shown by photoelectrochemical experiments under sunlight. Therefore, the
prepared films would have an advantage in water photolysis utilizing sunlight.
1 Introduction
As a renewable and clean energy source, solar energy is one of
the most promising future energy resources. Sunlight can be
transformed into electrical energy by photovoltaic cells and
stored as chemical energy in a storage battery or in the form of
hydrogen by the electrolysis of water.1 Especially, water
oxidation driven by sunlight has received great attention because
of its potential as a technology for the production of green fuel.2
Following the discovery of light-induced water-splitting with a
TiO2 semiconductor photoanode under ultraviolet irradiation in
1972,3 there has been considerable interest in the photoelec-
trolysis of water with photoelectrochemical cells. This process
results in oxygen evolution at the semiconductor photoanode
and hydrogen evolution at the cathode.4 Up to now, a number of
semiconductor materials have been focused on utilization of
solar energy. Especially, TiO2 is a traditional material for the
photoanode, which has become a benchmark material for
understanding the photo-oxidation process in the water splitting
reaction.3–15 However, the wide band gap of TiO2 (3 eV) is out of
the visible light region and only a small fraction of the solar
spectra can be utilized, which makes the final photoenergy
conversion factor less than 1%.16 From the viewpoint of solar
energy utilization, the development of photoelectric materials
to split water efficiently under visible light is indispensable.
Thus, new classes of semiconductor materials, such as Fe2O3
(Eg = 2.1 eV), WO3 (Eg = 2.5 eV) and FeS2, are continuously
being tested in order to use the less energetic but more abundant
visible light.1,16–19
FeS2 has two crystal phases: pyrite and marcasite. Marcasite
(Eg = 0.34 eV) is a metastable phase, which isn’t applied to the
process of photoelectric translation due to its small energy band
gap. However, pyrite, as a cubic,20 has a suitable energy band
gap (Eg = 0.95 eV) for the solar spectra. It has excellent electron
mobility and high light absorption coefficient (a > 105 cm21 for
l ¡ 700 nm), and its optical absorption coefficient is two orders
of magnitude higher than that of crystalline silicon.21 These
characteristics make pyrite a potential candidate as an absorber
material for thin-film solar cells, photovoltaic cells and water
photooxidation.22–24 However, the structure of its interface and
the presence of bulk defects (point defects, dislocations) provide
pathways for recombination and transfer of electrons through
interfacial barriers. So extrinsic and intrinsic properties of pyrite
still remain to be improved.25 In order to obtain better
photoelectric properties, there are two main approaches, one is
to develop new methods for preparing pyrite with a pure phase.
The select synthesis of uniform FeS2 octahedral and cubic
crystallites could be prepared by a facile surfactant-assisted
ethylene glycol-mediated solvothermal approach.26 More
Recently, J. Puthussery et al.27 used a simple hot-injection and
subsequent partial ligand exchange route to synthesize phase-
pure, single-crystalline, and well-dispersed colloidal pyrite
nanocrystals inks, which were then fabricated by sintering layers
at 500–600 uC under a sulfur atmosphere to obtain polycrystal-
line pyrite thin films. The other approach is to synthesize
transition metals doped pyrite. Several different dopants have
already been reported, such as Co,28 Ti,29 Ni,30 Cu31 or Zn.25
For these elements, both FeS2 and CoS2 crystallize in the pyrite
structure and constitute a mixed crystal system of general
composition Fe12xCoxS2 for (0 , x , 1).32–34 Recently, some
technologies have been developed to produce thin pyrite films,
such as evaporated iron layer,35 ion beam magnetron sputter-
ing,36 spray pyrolysis,37 electrodeposition38 and magnetron
School of Chemistry and Chemical Engineering, Sun Yat-Sen University,Guangzhou, 510275, P. R. China. E-mail: [email protected];Fax: +86-020-84112245; Tel: +86-020-84115559{ Electronic supplementary information (ESI) available. See DOI:10.1039/c1ra00066g
RSC Advances Dynamic Article Links
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sputtering.39 For all those methods, not only is the reaction
temperature very high, but also the prepared samples are largely
dependent on the equipment. Moreover, many sulfides, such as
Fe3S4, Fe7S8, FeS, would be easily produced during the reaction
process. Thus, further efforts should be devoted to investigating
green and simple synthesis routes to produce pyrite and Co-
doped FeS2 films.
As a preferred green solvent to traditional organic solvents,
supercritical carbon dioxide (scCO2) has been used in materials
science and industrial processes owing to its low viscosity, high
diffusivity, nontoxicity, nonflammability, low cost and recycl-
ability, etc. In the system of scCO2 and water, CO2 dissolves in
water to form carbonic acid, thereby decreasing the pH value to
2.8–3.0 during the reaction process;40–42 and water–CO2 (W/C)
microemulsions have been formed with specially designed
surfactants.42 These properties are attractive for studying the
formation of nanoparticles using the system of water and scCO2
according to reports.40–43 Previously, our group has reported
nanosized materials synthesized with the aid of scCO2, which
showed a significant effect on the crystallization of products.40–42
Herein, FeS2 and Co-doped FeS2 films could be successfully
grown on iron substrates through the reaction of iron foil and
sulfur source with the mixed system. The detailed reaction
conditions, such as the pressure of the system, temperature and
time, were investigated, and the structure of the films obtained
was characterized. Furthermore, the prepared FeS2 and Co-
doped FeS2 films were utilized as photoanodes, which demon-
strated excellent properties for water splitting and photoelectric
response by sunlight. Interestingly, compared with conventional
dye-sensitized photoelectrodes, the films without dye sensitizer
had better photoelectric properties under simulated sunlight.
2 Experimental
2.1 Chemicals
Chemicals: All reagents were of analytical grade and used as
received. The chemicals used in the syntheses were sodium
tripolyphosphate (Na5P3O10, STPP), sodium thiosulfate penta-
hydrate (Na2S2O3?5H2O), sulfur (S), potassium hydroxide
(KOH), cobaltous chloride (CoCl2?6H2O), ethylene glycol and
methanol, all of which were purchased from the Shanghai
Reagent Company (P.R. China). The CO2 (purity: 99.95%) and
iron (Fe) foil (purity: 99.99%, thickness: 0.1 mm, 1.0 cm 60.5 cm) were provided by the Guangzhou Gas Company and
Alfa Aesar, respectively.
2.2 Synthetic method
Preparation of the FeS2 and Co-doped FeS2 films: In a typical
synthetic procedure, a certain amount of Na5P3O10 was completely
dissolved in 12 mL mixture solution (Vethylene glycol : Vdeionized water =
1 : 9) with stirring; 2.7919 g Na2S2O3?5H2O was added to the
solution after complete dissolution of Na5P3O10; 0.1800 g sulfur
powder was then injected into the solution with stirring. When the
Co-doped FeS2 film was prepared, 0.0134 g CoCl2?6H2O were
added to the solution. The prepared mixture was transferred into
the PTFE reactor with the top with a small hole, which allows CO2
to flow into the reactor, then a piece of Fe foil (1.0 cm 6 0.50 cm)
was placed in the solution. Finally, the PTFE reactor was putted
into the stainless steel autoclave which was then sealed. The
stainless steel container was filled up with CO2 with a compressor.
First, the reactor was purged with a flow of CO2 to remove any
entrapped air from the autoclave and then filled with liquid CO2
to a desired amount using a high-pressure compressor. After
charging, the autoclave was slowly heated to the desired
temperature (FeS2: 160 uC; Co-doped FeS2: 180 uC), the pressure
of reaction system should be controlled under 11 MPa. The
reaction was maintained for 24 h. At the end of reaction, the
autoclave was cooled to room temperature, and then CO2 was
slowly vented through a pressure valve. The Fe foil was taken out
of solution, washed with deionized water followed by ethanol
three times, and finally air-dried for characterization. The detailed
experimental conditions for the synthesis of the samples are
listed in Table 1.
2.3 Characterization
The X-ray diffraction (XRD) pattern was recorded on a D8
(Bruker, Germany) X-ray diffractometer with graphite mono-
chromator Cu Ka radiation (l = 1.54178) operating at 40 kV
and 40 mA. Scanning electron microscopy (SEM) and energy-
dispersive X-ray spectroscopy (EDS) were carried out with thermal
field emission environmental SEM–EDS–EBSD (Quanta 400F,
Holand). The EDS and transmission electron microscopy (TEM)
image, selected area electron diffraction (SAED) pattern and high-
resolution transmission electron microscopy (HRTEM) image
were performed on a JEM-2010HR field emission transmission
electron microscope (JEOL, Japan). UV–vis absorption spectrum
was measured on UV–vis–NIR Spectrophotometer UV-3150
(SHIMADZU, Japan). All the measurements were performed at
room temperature.
2.4 Photoelectrochemical characterization
Photocurrents were measured in a three-electrode configuration
with 1 mol?L21 KOH (Containing 10% methanol, 25 C, pH =
13.6) as electrolyte, Ag/AgCl/ sat. KCl as reference, and a
platinum wire as counter electrode, separated by glass frits.
Contact to the Fe substrate of the FeS2 film was made with a Cu
clip wire above the electrolyte. The current of photoelectro-
chemical and photoelectric response were measured by an
Table 1 The experimental parameters for the synthesis of FeS2 and Co-doped FeS2 films on the iron foila
No. mSTPP mCoCl2T p t Vegw Phase
S1 2.0693 0 160 11 24 1 : 9 FeS2
S2 2.0693 0 160 6 24 1 : 9 FeS2
S3 2.0693 0 160 0 24 1 : 9 FeS2 + Fe7S8
S4 2.0693 0 160 11 24 0 : 10 FeS2 + XS5 2.0693 0 160 11 24 1 : 4 FeS2 + XS6 0 0 160 11 24 1 : 9 FeS2 + Fe7S8
S7 1.0347 0 160 11 24 1 : 9 FeS2 + Fe7S8
S8 2.0693 0 160 11 36 1 : 9 FeS2 + Fe7S8
S9 2.0693 0 160 11 48 1 : 9 FeS2 + Fe7S8 + XS10 2.0693 0 180 11 24 1 : 9 FeS2 + XS11 2.0693 0.0107 160 11 24 1 : 9 FeS2 + Fe7S8
S12 2.0693 0.0107 180 11 24 1 : 9 Co-doped FeS2
a mSTPP and mCoCl2in g, mCoCl2
= mCoCl2?6H2O; T in oC; p in MPa, p= 0
means No CO2 in the reaction system; t in hours; Vegw =Vethylene glycol:Vdeionized water; X = unknown phases.
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electrochemical workstation (CHI750B) under simulated sun-
light illumination. The potential of the photoelectrode is
reported against the reversible hydrogen electrode (RHE):
ERHE = EAgCl + 0.059pH + EuAgCl with EuAgCl = 0.1976 V at 25 uC
Sunlight was simulated using a Keithley 2400 source meter under
simulated AM 1.5 G illumination (100 mW?cm22) provided by
solar simulator (69920, 1 kW Xe lamp with optical filter, Oriel).
3 Results and discussion
3.1 Synthesis of the FeS2 and Co-doped FeS2 films in scCO2
The phases of the iron sulfide products were characterized by
XRD. Fig. 1 (S1 and S2) shows the XRD patterns of films
prepared in the presence of CO2 at 160 uC. All peaks match quite
well with the Joint Committee on Powder Diffraction Standards
(JCPDS) card 42-1340, and no additional peaks were found. The
result confirmed the formation of pure FeS2 crystals. S2 was
obtained under 6 MPa, the peaks of S2 indicated that the
product was pyrite. But S1 showed a good crystallinity compared
with S2. However, peaks of FeS2 and Fe7S8 (JCPDS: 25-0411)
were found when the reaction was conducted at 160 uC in the
absence of CO2 (Fig. 1 S3). When deionized water without
ethylene glycol was used as the solvent, an unknown phase is
observed in the product (S4); when the proportion of ethylene
glycol was increased (Vethylene glycol:Vdeionized water = 1 : 4), more
peaks of unknown phase could be seen in Fig. 1 (S5).
Indubitably, these results demonstrated that the CO2 and
ethylene glycol showed a significant effect on the crystallization
of pyrite.
Furthermore, CO2 and ethylene glycol not only have an
important effect on the phase formation, but also exert a key
influence on the morphology of product. The diverse morpho-
logies of Samples 1–5 can be obtained at different experimental
conditions (Fig. 2). A low-magnification SEM image of the
product obtained under 11 MPa is shown in Fig. 2a. The FeS2
film consists of a nanorod, a uniform nanorod with a length in
the range 0.5–1 mm and less than 100 nm in diameter can be
observed. Fig. 2b is an enlarged SEM image of the grain part of
Fig. 2a, from which the number of ridges on the film can be
clearly seen. The thickness of ridge top is less than 100 nm, much
thinner than the bottom thickness. As seen from Fig. 2c, when
the reaction pressure was reduced to 6 MPa, particles with
different sizes and morphologies could be found. When the CO2
pressure decreased to 0 MPa, namely CO2 wasn’t employed,
irregular particles including large size grains and rods were
prepared, which can be clearly observed in Fig. 2d. Similarly,
when ethylene glycol wasn’t added into the solvent, Sample 4
was made of polyhedron and small particles (Fig. 2e); when
2.4 mL ethylene glycol was injected into the solvent, irregular
grains are obtained and the size was larger than 1 mm (Fig. 2f).
The evident differences in the phase and morphology obtained
suggest that the CO2 and ethylene glycol could play an important
role in both the crystal phase and alignment of samples. This
could be interpreted below: the release rates of H+ ions and Fe2+
ions from iron substrates were possibly affected by the pH value
of the solution, since scCO2 dissolves into water to form carbonic
acid. Furthermore, the pH value can be controlled by changing
the pressure of CO2, namely, the release rates of both H+ ions
and Fe2+ ions can be easily adjusted by varying the CO2
pressure, and therefore the morphology of FeS2 was controlled
by regulating the pressure of the reaction system. A similar result
was reported previously.40 As for ethylene glycol, on the one
hand, it dissolved in water and changed the solubility of CO2 in
the solution mixture, and then the pH value of the solution was
adjusted; on the other hand, it could affect the solubility of S in
Fig. 1 The XRD patterns of samples: (S1) Sample 1; (S2) Sample 2; (S3)
Sample 3; (S4) Sample 4; (S5) Sample 5. *, + and X denote Fe, Fe7S8 and
unknown phase, respectively.
Fig. 2 The SEM images of samples. (a) SEM images of Sample 1; (b) is
enlarged picture of (a); (c) Sample 2; (d) Sample 3; (e) Sample 4; (f)
Sample 5.
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the solution mixture. The formation of FeS2 is represented by the
following equations:
CO2zH2O'H2CO3'HzzHCO3{ (1)
Fez2Hz~Fe2zzH2: (2)
Fe2zzS2O32{zSzH2O~FeS2zSO4
2{z2Hz (3)
The results demonstrate that variations in reaction conditions
including the additive, pressure, reaction temperature and doped
reagent, result in dramatic differences in the form and crystal
phases of the FeS2 and Co-doped FeS2 films (Table 1). In the
current synthetic system, the STPP played also an important role
in crystallization of FeS2. As shown in Fig. 3 S6, mixed phases
including FeS2, Fe7S8, etc., were prepared without STPP; when
1.0347 g STPP was injected into the solution, the diffraction
peaks of Fe7S8 were still found in the XRD pattern (Fig. 3 S7).
When STPP was increased to 2.0693 g, pure pyrite FeS2 was
successfully synthesized at last. The result indicates that the
STPP may be a favourable factor for the formation of pyrite,
which hasn’t been reported previously in the literature.
Furthermore, to investigate the evolution of morphology with
time, synthetic experiments with different reaction times were
conducted. When 36 h was adopted, one can see the peaks of
Fe7S8 in the pattern (Fig. 3 S8); when the reaction time was
increased to 48 h, the peaks of Fe7S8 and unknown phase can be
found (Fig. 3 S9). Thus, 24 h was appropriate to prepare the
rod-like nanostructured pyrite in this work. As an important
experimental parameter, different reaction temperatures were
adopted to synthesize the samples. Sample 10 was prepared at
180 uC. It is evident in S10 that the peaks at 2h of 23.2, 37.8 and
56.3 can’t be indexed to correspond to the sulfide from Fig. 3.
Thus, unknown compounds were prepared in S10 besides pyrite.
It is well known that pure pyrite films show p-type conduction,
and doping is necessary to obtain n-type conduction. The
improvement of electronic properties directly relates to the
distribution of dopant across the pyrite film.32 Therefore,
experiments were designed to produce n-type conduction in
pyrite through doping cobalt in scCO2 and water. When 0.0107 g
CoCl2 was injected into the solution, Co-doped FeS2 film could
be prepared at 160 uC. However, as shown in Fig. 3 S11, more
peaks of Fe7S8 could be clearly observed besides peaks of FeS2.
Surprisingly, only the doped pyrite film was obtained at 180 uC(Fig. 3 S12). This fact indicated that the doping procedure for
pyrite by Co needs higher temperature in the same reaction
medium. The element component of prepared Sample 12 was
recorded by energy-dispersive X-ray spectroscopy (EDS). As
seen in Fig. 4a, the EDS demonstrates that the product consists
of three elements. The Fe peaks at about 0.7 and 6.4 keV, Co
peak at about 0.7 keV and the S peak at 2.4 keV are observed.
The Fe, Co and S atomic percentages are analyzed to be 30.39%,
1.49% and 68.12%, respectively. The EDS analysis of the
compound reveals that the product is mainly composed of Fe,
Co and S and its atomic ratio is about 0.985 : 0.015 : 2. Fig. 4b
shows a low-magnification SEM image of the Co-doped FeS2
film (S12), indicating the close layer consists of lager particles,
the top of which has plenty of subulate ridges. An enlarged SEM
image shown in Fig. 4c suggests that the surface of the film
scatters lots of ridges and its top of thickness is less than 100 nm.
Compared with S1 prepared at 160 uC, the thickness of ridge
(S12) is much larger. The above results indicate that the higher
temperature is necessary for the Co doping into the pyrite crystal
lattice. But their products have a similar morphology.
The FeS2 and Co-doped FeS2 films were further investigated
by TEM shown in Fig. 5 displaying a more detailed structure of
the crystal. Fig. 5a confirms the taper morphology of FeS2, and
lots of the particles assemble into the film. The thickness of the
top is much thinner than that of the bottom. The result is in good
agreement with structures obtained from SEM observation
mentioned above in Fig. 2a and b. The top inset SAED pattern
corresponding to the tip (1 region), the (111), (200) and (111)
planes of FeS2 (JCPDS 42-1340) are determined from the sharp
spots due to the [022] zone, which demonstrates it has a single
crystal structure. The corresponding HRTEM image shows the
clear crystal lattice planes (Fig. 5b), which also have been
obtained from [022]–projected. The fringe space is determined to
Fig. 3 The XRD patterns of other samples: (S6) Sample 6; (S7) Sample
7; (S8) Sample 8; (S9) Sample 9; (S10) Sample 10; (S11) Sample 11; (S12)
Sample 12. *, + and X denote Fe, Fe7S8 and unknown phase,
respectively.
Fig. 4 (a) The energy-dispersive X-ray spectrum for S12; (b) the SEM
image of S12; and (c) is the enlarged picture of (b).
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be 0.31 nm, which is in accordance with the (111) lattice spacing of
FeS2. The TEM image (Fig. 5c) clearly shows the size and
morphology of Co-doped FeS2 particles. The EDS shows that the
components of product are Fe, Co and S (Fig. 5 in the ESI{). As
seen from the corresponding HRTEM image of the 2 region
(Fig. 5d), the top of the inset corresponding to fast fourier trans-
form (FFT), and the clear lattice fringes reveal a good crystallinity.
3.2 The properties of photoelectric response and water photolysis
The optical property of FeS2 and Co-doped FeS2 films was
determined by UV-vis absorption spectroscopy. As shown in
Fig. 6, the larger absorption of S1 and S12 starts from around
600 nm and it reaches saturation at about 450 nm. As we know,
when the size of the product grains is considerably larger,
quantum-confinement effects seem inexistent. However, com-
pared with the direct band gap 0.9 eV (l = 1375 nm) of bulk
FeS2,44 the current experimental results show that the absorption
edge has an obvious blue shift, indicating the strong quantum
confinement of FeS2 and Co-doped FeS2 films. It can be
concluded that the reason would be that quantum-confinement
effects possibly occur near the peak edge of the tips, which are
thinner, since the optical properties of non-spherical nanocrys-
tals are controlled by the lowest dimension of nanocrystals.42
To investigate the electron-transfer process, several sets of
photoelectrochemical experiments were carried out to measure
the photocurrent response of the films. Potentiostatic (current
and time) experiments were conducted to check the photo-
response properties of the films. Fig. 7a shows the photocurrent
and dark current transients obtained using the films as photo-
anodes. The experimental equipment ran for 100 s firstly, then
the illuminating time was taken for 10 s each time. When the
Fig. 5 (a) TEM image of sample 1. The top inset is SAED pattern
corresponding to 1 region; (b) HRTEM image corresponding to 1 region;
(c) TEM image of sample 12; (d) HRTEM image corresponding to 2
region, the top inset is its FFT.
Fig. 6 UV-vis absorption spectra of S1 and S12.
Fig. 7 (a) Photocurrent response and (b) Current–voltage behavior of
Fe, FeS2 (S1) and Co-doped FeS2 (S12) films under the darkness and
illumination of simulated sunlight. Light intensity: 100 mW?cm22;
electrolyte: 1 mol?L21 KOH containing 10% methanol.
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electrodes were illuminated by simulated sunlight, the increase
in the current density for FeS2 film was 0.50 mA?cm22, but it
was about 1.0 mA?cm22 for Co-doped FeS2 film; when the
illumination was interrupted, the current density rapidly
dropped to the original value of steady state. The current
responded with the turn-on and turn-off of the light quickly.
Compared with the photoelectric response of synthesized films,
the photocurrent wasn’t produced when the iron film was
illuminated. Up to now, the photoelectric response of lots of
materials have been reported in the literature, such as
Ru(dcbpy)2(NCS)2 sensitized ZnO, polyoxophosphotungstate-
TiO2/Ti under UV pulse illumination and Tl2O3 films in the
1 mol?L21 KOH containing 0.18 mol?L21 TlAc.45–47 Although
the FeS2 and Co-doped FeS2 films weren’t sensitized, their
photoelectric response could be displayed under simulated
sunlight. And these films could be suitable for application
under sunlight.
Fig. 7b displays the current–voltage (I–V) curves of Fe, FeS2
and Co-doped FeS2 films under darkness and simulated sunlight,
respectively. The current of Fe film wasn’t measured under both
of darkness and sunlight up to about 1.4 VRHE. The current of
FeS2 film could be determined at 0.94 VRHE under darkness at
first, then the current rises slowly to 19.5 mA?cm22 at 1.1 VRHE
and it remains almost constant until 1.4 VRHE. Corresponding to
the potential of the reversible oxygen electrode, the current
density is 21.6 mA?cm22 at 1.23 VRHE; the photocurrent of FeS2
film would be produced at 0.90 VRHE under sunlight and the
cathodic shift of voltage value is about 0.04 V. The photocurrent
rapidly increased and the current density reached 42.5 mA?cm22.
Under similar conditions, the current of Co-doped FeS2 film is
produced at about 0.94 VRHE under darkness. The current
density rapidly goes up to 42.5 mA?cm22 at 1.23 VRHE, which is
almost twice of FeS2 film. Surprisingly, the photocurrent would
be determined at 0.72 VRHE under sunlight and the cathodic shift
is about 0.22 V which is much larger than that of FeS2. The
photocurrent steeply climbed and the current density arrived to
56.8 mA?cm22 under sunlight, which is larger than that of FeS2
under illumination condition. The photocurrent density of FeS2
and Co-doped FeS2 is higher than that of reported materials
such as Fe2O3 and TiO2.1,48,49
Based on the current experimental results and reports,49,50 the
possible schematic of water splitting would be deduced to
understand how the prepared films help to split water. Step I, the
films absorbs photon energy which is greater than the band gap
energy of the material, then photoexcited electrons and holes
pairs are generated on the films; step II, electrons and holes
would immediately reach the surface of the films; Step III,
CH3OH, which was adsorbed by the surface of the films, would
be easily oxidized by holes to CO2 in the surface (CH3OH can be
easily oxidized than water). The electrons flow toward the
substrate (Fe) and pass to the cathode (Pt) through the external
circuit, which induced H2O to be reduced, and then H2 would be
generated. The first step is strongly dependent on the structure
and electronic properties of the materials. Especially, a number
of photoexcited electrons and holes can recombine in the second
step, which largely reduces the photooxidation ability. In this
study, on the one hand, CH3OH, a sacrificial reagent, promoted
H2 evolution by its preferential photooxidation. And it relatively
decreases the rate of the surface recombination between the
surface hole and electron pairs because the concentration of
holes on the surface decreases as to capture holes; on the other
hand, the iron substrate has better electric conductivity than the
prepared films. The electrons can easily reach the Fe substrate,
which reduce the electrons and holes recombination loss.
Consequently, the presence of CH3OH and the use of substract
(Fe) promote H2 evolution under illumination because of
decrease in the surface recombination rate of the electron and
hole. Thus, compared with the literature reported,1,48,49 the
photocurrent density of FeS2 and Co-doped FeS2 is higher.
In addition, electron paramagnetic resonance suggested that
Co2+ substituting Fe2+ in the pyrite structure introduces defect
states at different energy levels within the forbidden zone.51 The Co
defect state with a donor electron occurs in the band gap, near or
possibly overlapping the conduction band energy, so the extra
electrons easily move into the conduction band. Furthermore,
cobalt would play a catalytic role during the photocurrent process.
The electrocatalytic activity of cobalt and iron/cobalt oxides for
water oxidation is well established and involves the CoII/CoIII and
CoIII/CoIV couples.1,52,53 The distinct photocurrent response and
photocurrent density of the FeS2 and Co-doped FeS2 can be
attributed to the cobalt doped in the pyrite.
Conclusions
Pyrite FeS2 and Co-doped FeS2 films were synthesized with the
aid of scCO2. Diverse phases and morphologies could be
obtained by controlling different reaction conditions. The
reaction conditions including the pressure, precursor, STPP,
reaction temperature and doped reagent, result in dramatic
differences in the crystal phases. The UV-vis absorption
spectroscopy of these films indicated that the absorption
wavelength has an obvious blue shift compared with bulk
FeS2. Photoelectrochemical experiments were conducted to
measure the photocurrent response of the films. The current
increase of FeS2 films was 0.5 mA?cm22, and the current increase
of Co-doped FeS2 films was about 1 mA?cm22 under sunlight.
As shown in the current–voltage (I–V) curve, the current density
of FeS2 achieved 42.5 mA?cm22 at 1.23 VRHE and the cathodic
shift of voltage value was about 0.04 V under sunlight. The
doped Co2+ electrode resulted in a 0.22 V cathodic shift, and
the photocurrent increased to 56.8 mA.cm22 at 1.23 VRHE. The
present study has demonstrated that the FeS2 and Co-doped
FeS2 films prepared display excellent properties for photoelectric
response and water photolysis under sunlight.
Acknowledgements
We gratefully appreciate the assistance with the photoelectro-
chemical characterization of Mr. Bingxin Lei and Mr. Xihong Lu.
References
1 A. Kay, I. Cesar and M. Gratzel, J. Am. Chem. Soc., 2006, 128,15714.
2 J. A. Turner, Science, 1999, 285, 687.3 A. Fujishima and K. Honda, Nature, 1972, 238, 37.4 M. Gratzel, Nature, 2001, 414, 338.5 A. J. Nozik, Nature, 1975, 257, 383.6 Z. W. Qu and G. J. Kroes, J. Phys. Chem. B, 2006, 110, 23306.7 I. J. Ferrer, H. Mukaki and P. Salvador, J. Phys. Chem., 1986, 90, 2805.
260 | RSC Adv., 2011, 1, 255–261 This journal is � The Royal Society of Chemistry 2011
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nloa
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on 2
8 M
ay 2
012
Publ
ishe
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Aug
ust 2
011
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ttp://
pubs
.rsc
.org
| do
i:10.
1039
/C1R
A00
066G
View Online
8 A. L. Linsebigler, G. Lu and J. T. Yates, Jr, Chem. Rev., 1995, 95,735.
9 L. Kavan, M. Gratzel, S. E. Gilbert, C. Klemenz and H. J. Scheel,J. Am. Chem. Soc., 1996, 118, 6716.
10 R. Nakamura and Y. Nakato, J. Am. Chem. Soc., 2004, 126, 1290.11 R. Nakamura, T. Okamura, N. Ohashi, A. Imanishi and Y. Nakato,
J. Am. Chem. Soc., 2005, 127, 12975.12 B. Neumann, P. Bogdanoff, H. Tributsch, S. Sakthivel and H. Kisch,
J. Phys. Chem. B, 2005, 109, 16579.13 F. Allegretti, S. O’Brian, M. Polcik, D. I. Sayago and D. P.
Woodruff, Phys. Rev. Lett., 2005, 95, 226104/1.14 G. Mattioli, F. Filippone and A. A. Bonapasta, J. Am. Chem. Soc.,
2006, 128, 13772.15 T. Bak, J. Nowotny, M. Rekas and C. C. Sorrell, Int. J. Hydrogen
Energy, 2002, 27, 991.16 A. Valdesa and G. J. Kroes, J. Chem. Phys., 2009, 130, 114701/1.17 Z. Zou, J. Ye, K. Sayama and H. Arakawa, Nature, 2001, 414, 625.18 C. Santato, M. Ulmann and J. Augustynski, Adv. Mater., 2001, 13,
511.19 W. Jaegermann and H. Tributsch, J. Appl. Electrochem., 1983, 13,
743.20 A. K. Kleppe and A. P. Jephcoat, Mineral. Mag., 2004, 68, 433.21 A. Ennaoui, S. Fiechter, C. Pettenkofer, N. Alonso-Vante, K. Buker,
C. Hapfner and H. Tributsch, Sol. Energy Mater. Sol. Cells, 1993, 29,289.
22 A. Ennaoui, S. Fiechter, H. Goslowsky and H. Tributsch,J. Electrochem. Soc., 1985, 132, 1579.
23 Y. Hu, Z. Zheng, H. M. Jia, Y. W. Tang and L. Z. Zhang, J. Phys.Chem. C, 2008, 112, 13037.
24 H. Duan, Y. F. Zheng, Y. Z. Dong, X. G. Zhang and Y. F. Sun,Mater. Res. Bull., 2004, 39, 1861.
25 K. Buker, S. Fiechter, V. Eyert and H. Tributsch, J. Electrochem.Soc., 1999, 146, 261.
26 D. W. Wang, Q. H. Wang and T. M. Wang, CrystEngComm, 2010,12, 755.
27 J. Puthussery, S. Seefeld, N. Berry, M. Gibbs and M. Law, J. Am.Chem. Soc., 2011, 133, 716.
28 J. Oertel, K. Ellmer, W. Bohne, J. Rohrich and H. Tributsch,J. Cryst. Growth, 1999, 198(199), 1205.
29 A. Pascual, P. Dıaz-Chao, I. J. Ferrer, C. Sanchez and J. R. Ares, Sol.Energy Mater. Sol. Cells, 2005, 87, 575.
30 S. Lehner, K. Savage, M. Ciobanu and D. E. Cliffel, Geochim.Cosmochim. Acta, 2007, 71, 2491.
31 I. J. Ferrer, C. de las Heras and C. Sanchez, Appl. Surf. Sci., 1993,70(71), 588.
32 P. Dıaz-Chao, I. J. Ferrer and C. Sanchez, Thin Solid Films, 2008,516, 7116.
33 R. J. Bouchard, Mater. Res. Bull., 1968, 3, 563.34 S. Ogawa and T. Teranishi, Phys. Lett. A, 1972, 42, 147.35 B. Rezig, H. Dahman and M. Kenzari, Renewable Energy, 1992, 2,
125.36 M. Birkholz, D. Lichtenberger, C. Hopfner and S. Fiechter, Sol.
Energy Mater. Sol. Cells, 1992, 27, 243.37 B. Thomas, K. Ellmer and M. Muller, J. Cryst. Growth, 1997, 170,
808.38 S. Nakamura and A. Yamamoto, Sol. Energy Mater. Sol. Cells, 2001,
65, 79.39 G. Willeke, R. Dasbach and B. Sailer, Thin Solid Films, 1992, 213,
271.40 J. Q. Jiao, L. P. Chen, X. Liu, W. Gao and F. J. Feng, Mater. Res.
Bull., 2009, 44, 1161.41 J. Q. Jiao, X. Liu, W. Gao, C. W. Wang, F. J. Feng, X. L. Zhao and
L. P. Chen, Solid State Sci., 2009, 11, 976.42 J. Q. Jiao, X. Liu, W. Gao, C. W. Wang, H. J. Feng, X. L. Zhao and
L. P. Chen, CrystEngComm, 2009, 11, 1886.43 K. T. Lim and H. S. Hwang, Langmuir, 2004, 20, 2466.44 P. Gao, Y. Xie, L. N. Ye, Y. Chen and Q. X. Guo, Cryst. Growth
Des., 2006, 6, 583.45 Y. B. Xie, Adv. Funct. Mater., 2006, 16, 1823.46 M. Yang, D. J. Wang, L. Peng, T. F. Xie and Y. Y. Zhao,
Nanotechnology, 2006, 17, 4567.47 J. F. Liu, Z. H. Lu, S. Y. Zhao and K. Z. Yang, Supramol. Sci., 1998,
5, 541.48 S. E. John, S. K. Mohapatra and M. Misra, Langmuir, 2009, 25,
8240.49 S. K. Mohapatra, S. E. John, S. Banerjee and M. Misra, Chem.
Mater., 2009, 21, 3048.50 K. Izawa, T. Yamada, U. Unal, S. Ida, O. Altuntasoglu,
M. Koinuma and Y. Matsumoto, J. Phys. Chem. B, 2006, 110, 4645.51 R. N. Chandler and R. W. Bene, Phys. Rev. B, 1973, 8, 4979.52 B. S. Brunschwig, M. H. Chou, C. Creutz, P. Ghosh and N. Sutin,
J. Am. Chem. Soc., 1983, 105, 4831.53 Y. Matsumoto and E. Sato, Mater. Chem. Phys., 1986, 14, 397.
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