Synthesis of large surface area LaFeO3 nanoparticles by SBA-16 ...
Synthesis of large surface area LaFeO3 nanoparticles by SBA-16 ...
Synthesis of large surface area LaFeO3 nanoparticles by SBA-16 ...
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J Nanopart Res<br />
DOI 10.1007/s11051-009-9647-5<br />
RESEARCH PAPER<br />
<strong>Synthesis</strong> <strong>of</strong> <strong>large</strong> <strong>surface</strong> <strong>area</strong> LaFeO 3 <strong>nanoparticles</strong><br />
<strong>by</strong> <strong>SBA</strong>-<strong>16</strong> template method as high active visible<br />
photocatalysts<br />
Haijiao Su Æ Liqiang Jing Æ Keying Shi Æ<br />
Changhao Yao Æ Honggang Fu<br />
Received: 25 October 2008 / Accepted: 28 April 2009<br />
Ó Springer Science+Business Media B.V. 2009<br />
Abstract Nanosized LaFeO 3 with <strong>large</strong> specific<br />
<strong>surface</strong> <strong>area</strong> has been successfully synthesized <strong>by</strong> an<br />
impregnation process, with mesoporous silica <strong>SBA</strong>-<strong>16</strong><br />
as hard template and corresponding metal nitrates as<br />
La and Fe resources, and the resulting LaFeO 3 is also<br />
characterized <strong>by</strong> thermogravimetry–differential thermal<br />
analysis (TG–DTA), X-ray diffraction (XRD), N 2<br />
adsorption–desorptions, Brunauer Emmett Teller<br />
(BET) technique, transmission electron microscopy<br />
(TEM), X-ray photoelectron spectroscopy (XPS),<br />
UV–visible diffuse reflection spectrum (UV–Vis<br />
DRS), and <strong>surface</strong> photovoltage spectroscopy (SPS).<br />
It is found that, compared with that prepared <strong>by</strong> the<br />
conventional citrate method, the as-prepared LaFeO 3<br />
with 20-50 nm particle size has remarkable <strong>large</strong><br />
specific <strong>surface</strong> <strong>area</strong>, even still with the <strong>surface</strong> <strong>area</strong> as<br />
<strong>large</strong> as about 85 m 2 g -1 after calcination at 800 °C,<br />
which is attributed to its mesoporous structure as well<br />
as the small particle size. During the photocatalytic<br />
degradation <strong>of</strong> Rhodamine B solution under visible<br />
H. Su L. Jing (&) K. Shi C. Yao H. Fu (&)<br />
Key Laboratory <strong>of</strong> Functional Inorganic Materials<br />
Chemistry, Ministry <strong>of</strong> Education, Heilongjiang<br />
University, Harbin 150080, People’s Republic <strong>of</strong> China<br />
e-mail: Jinglq@hlju.edu.cn<br />
H. Fu<br />
e-mail: Fuhg@vip.sina.com<br />
irradiation, all the LaFeO 3 samples obtained are<br />
superior to P25 TiO 2 , and the activity becomes high<br />
with increasing calcination temperature. It is revealed<br />
that the excellent photocatalytic performance is<br />
mainly ascribed to the <strong>large</strong> <strong>surface</strong> <strong>area</strong> and high<br />
photogenerated charge separation rate.<br />
Keywords LaFeO 3 Nanoparticle <br />
<strong>SBA</strong>-<strong>16</strong> template method Visible photocatalysis<br />
Introduction<br />
In recent years, nanoscale structures have attracted<br />
extensive attention as a result <strong>of</strong> their novel sizedependent<br />
properties (Wang and Herron 1991; Guldi<br />
et al. 2005; Gleiter et al. 2001). Most <strong>of</strong> the research<br />
efforts which were concentrated on the mixed metal<br />
oxides <strong>of</strong> the perovskite family, ABO 3 , where<br />
A = rare-earth and B = transition element, are important<br />
in advanced technologies such as fuel cells<br />
(Plonczak et al. 2008), catalysis (Arendt et al. 2008),<br />
electrode materials (Zhang et al. 2008), and sensors (Li<br />
et al. 2001). It has been observed that the perovskite<br />
oxides also function as good photocatalysts (Yang et al.<br />
2007). In the last two decades, the development <strong>of</strong><br />
photocatalysts with visible-light response has been<br />
studied extensively from the viewpoint <strong>of</strong> the utilization<br />
<strong>of</strong> solar light energy. Intense research activity in<br />
this <strong>area</strong> has resulted in many novel mixed metal oxide<br />
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J Nanopart Res<br />
photocatalysts for water splitting such as SrTiO 3 ,<br />
NaTaO 3 , etc. (Subramanian et al. 2006; Kato and Kudo<br />
2003; Maeda and Domen 2007; Penä and Fierro 2001),<br />
and the photocatalytic decompositions <strong>of</strong> organic<br />
compounds have been widely studied, but all the<br />
performance need to be advanced.<br />
The specific <strong>surface</strong> <strong>area</strong> and crystal structure are<br />
the most important two factors influencing catalytic<br />
activity. During several conventional synthetic processes<br />
<strong>of</strong> perovskites, such as citrate method and<br />
solid state reactions, the high-temperature thermal<br />
treatments needed usually lead to the sintering <strong>of</strong> the<br />
resulting particles, consequently decreasing greatly<br />
the specific <strong>surface</strong> <strong>area</strong>, which will <strong>large</strong>ly influence<br />
the performance <strong>of</strong> the resulting perovskites and<br />
hinder their widespread use as catalysts. Thus, novel<br />
synthetic methods to obtain materials with <strong>large</strong><br />
specific <strong>surface</strong> <strong>area</strong> are greatly desired.<br />
Among various preparation methods <strong>of</strong> nanosized<br />
materials, the template method, which provides a<br />
good choice for the synthesis <strong>of</strong> <strong>nanoparticles</strong> with<br />
controllable size and shape because <strong>of</strong> being in a<br />
confined three-dimensional (3D) space, has recently<br />
sparked great research interests (Lu and Schüth 2006;<br />
Schüth 2003). Unlike conventional surfactant templates,<br />
the hard template could effectively maintain<br />
the local strain caused <strong>by</strong> the crystallization <strong>of</strong><br />
precursors. Zhao et al. synthesized highly dispersed<br />
TiO 2 <strong>nanoparticles</strong> using <strong>SBA</strong>-15 as hard template<br />
(Zhao and Yu 2006). Valdés-Solís et al. prepared<br />
nanosized perovskites and spinels through a silica<br />
xerogel template route (Valdés-Solís et al. 2005).<br />
However, so far the articles on the use <strong>of</strong> the <strong>SBA</strong>-<strong>16</strong><br />
as hard template to synthesize nanosized solid<br />
materials are seldom reported. <strong>SBA</strong>-<strong>16</strong> is a kind <strong>of</strong><br />
3D, ‘‘cage-like’’ mesoporous silica, and its pores are<br />
connected <strong>by</strong> some mesoporous windows, so as to be<br />
beneficial for the substance transportation. Thus, it<br />
can be deduced that its negative replica is 3D<br />
connected structure (Shi et al. 2005a, b; Schüth and<br />
Schmid 2002; Kärger and Freude 2002), so that the<br />
<strong>SBA</strong>-<strong>16</strong> as template to prepare porous solid materials<br />
with <strong>large</strong> <strong>surface</strong> <strong>area</strong> is feasible. It has been<br />
demonstrated that mesoporous structure is highly<br />
desirable for effective photocatalysis, since such<br />
structures enable more light to be harvested and also<br />
possess continuous pore channels that facilitate the<br />
transfer <strong>of</strong> reactant molecules.<br />
As a kind <strong>of</strong> important functional material, LaFeO 3<br />
with a typical ABO 3 -type perovskite structure has<br />
many applications, such as catalytic oxidation, electrode<br />
materials, and chemical sensors for the humidity<br />
and alcohols, and it also is an ideal potential semiconductor<br />
material for visible photocatalyst because <strong>of</strong> its<br />
small band gap energy (Wang et al. 2006; Li et al.<br />
2007). Herein, nanosized LaFeO 3 with <strong>large</strong> <strong>surface</strong><br />
<strong>area</strong> was synthesized with mesoporous silica <strong>SBA</strong>-<strong>16</strong><br />
as hard template for the first time. The as-prepared<br />
LaFeO 3 exhibits excellent visible-light photocatalytic<br />
activity, which is attributed to the <strong>large</strong> <strong>surface</strong> <strong>area</strong>, as<br />
well as to the high photoinduced charge separation rate<br />
mainly based on the SPS responses. This should be<br />
valuable for the practical application <strong>of</strong> LaFeO 3 and<br />
also provides a new strategy to prepare other highperformance<br />
nanostructured oxide composite materials<br />
with <strong>large</strong> <strong>surface</strong> <strong>area</strong>.<br />
Experimental<br />
Preparation <strong>of</strong> the template <strong>SBA</strong>-<strong>16</strong><br />
The <strong>SBA</strong>-<strong>16</strong> was synthesized <strong>by</strong> a sol–gel process as<br />
described elsewhere (Shi et al. 2005a, b). The F127<br />
(EO 106 PO 70 EO 106 , BASF) and Ethyl silicate<br />
(C 8 H 20 O 4 Si) were used as surfactant and silicon<br />
sources, respectively. After the resulting xerogel was<br />
calcined at 550 °C with a heating rate <strong>of</strong> 1 °C min -1<br />
and ground, the mesoporous silica <strong>SBA</strong>-<strong>16</strong> was<br />
obtained eventually.<br />
<strong>Synthesis</strong> <strong>of</strong> the samples<br />
Nanosized LaFeO 3 was synthesized according to the<br />
flowchart shown in Fig. 1. First, 1 g <strong>of</strong> freshly<br />
as-synthesized <strong>SBA</strong>-<strong>16</strong> was dispersed in 2 mL <strong>of</strong><br />
ethanol solution, containing 0.0041 mol <strong>of</strong> La(NO 3 ) 3 <br />
6H 2 O and 0.0041 mol <strong>of</strong> Fe(NO 3 ) 3 9H 2 O. After<br />
ultrasonication for 10 min, the mixture obtained was<br />
kept at 60 °C under stirring until the solvent was<br />
evaporated completely. Subsequently, the LaFeO 3 –<br />
<strong>SBA</strong>-<strong>16</strong> composite was obtained after the above<br />
mixture was dried in a vacuum at 80 °C and calcined<br />
in air at needed temperature for 2 h. Finally, the<br />
template-free LaFeO 3 nanopowder was gained <strong>by</strong><br />
washing, drying, grinding, and heat-treatment at<br />
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J Nanopart Res<br />
La(NO 3 ) 3·6H 2 O<br />
Fe(NO 3 ) 3·9H 2 O<br />
Ethanol<br />
Nitrate ethanol solution<br />
Adding<br />
Fresh <strong>SBA</strong>-<strong>16</strong><br />
Mixed solution<br />
Drying and grinding<br />
precursor<br />
Calcining<br />
Template-containing LaFeO 3<br />
Washing, drying and calcining<br />
after treatment with NaOH<br />
Template-free LaFeO 3<br />
Fig. 1 Flowchart <strong>of</strong> the synthetic processes <strong>of</strong> nanosized<br />
LaFeO 3<br />
500 °C after the silica in the composite was dissolved<br />
in the 2 M NaOH solution.<br />
Characterization <strong>of</strong> the samples<br />
The thermogravimetry–differential thermal analysis<br />
(TG–DTA) <strong>of</strong> the dry mixtured precursor was<br />
performed using a Rigaku TAS 100 thermal analyzer,<br />
with the temperature rate <strong>of</strong> 10 °C min -1 in air,<br />
referenced to a-Al 2 O 3 . The crystal structure <strong>of</strong> the<br />
samples was determined <strong>by</strong> X-ray diffraction (XRD)<br />
method (Rigaku D/MAX-rA powder diffractometer,<br />
Japan). N 2 adsorption–desorption isotherm <strong>of</strong> the<br />
sample was carried out at the temperature <strong>of</strong> liquid<br />
nitrogen <strong>by</strong> using a Micromeritics ASAP 2020 M<br />
system, outgassed for 10 h at 300 °C prior to the<br />
measurements. Transmission electron microscopy<br />
(TEM) observation <strong>of</strong> the sample was performed on<br />
a JEM-3010 electron microscope (JEOL, Japan), with<br />
an acceleration voltage <strong>of</strong> 300 kV. The BET <strong>surface</strong><br />
<strong>area</strong> was evaluated <strong>by</strong> a ST-2000 constant volume<br />
adsorption apparatus. The <strong>surface</strong> composition and<br />
elemental chemical state <strong>of</strong> the samples were examined<br />
<strong>by</strong> X-ray photoelectron spectroscopy (XPS)<br />
using a Model VG ESCALAB apparatus with AlKa<br />
X-ray source. The binding energies were calibrated<br />
with respect to the signal for adventitious carbon<br />
(binding energy = 284.6 eV). The UV–visible diffuse<br />
reflection spectrum (UV–vis DRS) <strong>of</strong> the<br />
samples was recorded with Shimadzu UV-2550<br />
Spectrophotometer, using BaSO 4 as reference. The<br />
SPS measurement <strong>of</strong> the samples was carried out with<br />
a home-built apparatus that had been described<br />
elsewhere (Jing et al. 2003).<br />
Photocatalytic activity measurement<br />
Rhodamine B (C 28 H 31 ClN 2 O 3 ) is a common dye that is<br />
extensively used in a variety <strong>of</strong> industrial applications<br />
(Wang et al. 2008; Huang et al. 2003). Therefore, the<br />
photocatalytic activity <strong>of</strong> the as-synthesized samples<br />
was evaluated <strong>by</strong> photodegradation <strong>of</strong> Rhodamine B<br />
under irradiation <strong>of</strong> visible light (k [ 400 nm). The<br />
light source was a high-pressure Xe lamp (150 W).<br />
Light passed through a cut<strong>of</strong>f filter and then was<br />
focused onto a 100-mL beaker. The reaction was<br />
maintained at ambient temperature. In a typical<br />
experiment, aqueous suspensions <strong>of</strong> Rhodamine B<br />
and 0.10 g <strong>of</strong> the photocatalyst powder were placed in<br />
the beaker. Prior to irradiation, the suspension was<br />
magnetically stirred in the dark to ensure the establishment<br />
<strong>of</strong> an adsorption/desorption equilibrium. At<br />
given irradiation time, 10 mL <strong>of</strong> the suspension was<br />
collected and centrifuged to remove the particles; then,<br />
the dye concentration was determined <strong>by</strong> measuring<br />
the UV–Vis absorbance <strong>of</strong> the dye aqueous solution.<br />
Results and discussion<br />
Measurements <strong>of</strong> TG–DTA and XRD<br />
Figure 2 is the TG–DTA curves <strong>of</strong> the dry mixed<br />
powder obtained. There are three stages during the<br />
weight loss process, one is at the temperature range<br />
from the room temperature to 250 °C, with endothermic<br />
phenomenon, mainly attributed to desorption<br />
<strong>of</strong> water that is physically adsorbed. The next is from<br />
300 to 500 °C, with three maximum exothermic<br />
peaks, accompanied <strong>by</strong> drastic weight loss which was<br />
attributed to vaporization <strong>of</strong> inner water and autocombustion<br />
during the nitrate decomposition <strong>of</strong> the<br />
dried powder. There is a slight loss process at the<br />
temperature higher than 500 °C, which is mainly<br />
caused <strong>by</strong> desorption <strong>of</strong> residual hydroxyl (OH)<br />
group (Nosaka et al. 1998). In this case, the slight<br />
exothermic phenomenon can be seen, which is<br />
possibly attributed to the gradual crystallization <strong>of</strong><br />
LaFeO 3 .<br />
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Mass loss (%)<br />
Fig. 2<br />
100<br />
90<br />
80<br />
70<br />
60<br />
50<br />
40<br />
TG<br />
DTA<br />
Exo<br />
0<br />
Endo<br />
-2<br />
200 400 600 800 1000<br />
Temperature (°C)<br />
The XRD patterns <strong>of</strong> the as-prepared LaFeO 3<br />
samples calcined at different temperature are shown<br />
in Fig. 3. For the sample calcined at 500 °C, no<br />
obvious XRD peaks can be seen, indicating that there<br />
is mainly amorphous. When the calcination temperature<br />
is higher than 500 °C, the marked XRD peaks,<br />
which can be indexed to the ABO 3 -type LaFeO 3 as<br />
shown in the standard JCPDS No. 15-0148, display,<br />
and the XRD intensity gradually increases with<br />
enhancing the calcination temperature, implying that<br />
the crystallinity becomes much high.<br />
Measurements <strong>of</strong> N 2 adsorption–desorption,<br />
TEM, and BET<br />
In order to reveal the structure <strong>of</strong> the as-prepared<br />
LaFeO 3 , we took the measurements <strong>of</strong> N 2 adsorption–desorption<br />
and TEM observation <strong>of</strong> the sample<br />
10<br />
TG–DTA curves <strong>of</strong> the dry mixed powder obtained<br />
8<br />
6<br />
4<br />
2<br />
Heat flow (mV)<br />
calcined at 700 °C. Figure 4 shows the N 2 adsorption–desorption<br />
isotherm <strong>of</strong> the LaFeO 3 and pore size<br />
distributions (inset) calculated from desorption<br />
branch <strong>by</strong> the BJH method. The isotherm exhibits a<br />
long and narrow hysteresis loop, which is due to the<br />
nonstandard porous structure (Jin et al. 2006; Zapilko<br />
et al. 2007), and it can be seen that the template-free<br />
LaFeO 3 has disordered porous structure from the low<br />
values <strong>of</strong> dV/dR at BJH pore size distributions. The<br />
isotherm which starts a sharp capillary condensation<br />
step at low relative pressures must be caused <strong>by</strong> the<br />
pore size centered between 2 and 5 nm and has the<br />
hysteresis loop taken at high relative pressures<br />
attributed to its having <strong>large</strong> slit-like pores, size <strong>of</strong><br />
which extended to above 10 nm, between the particles<br />
rather than a mesostructure. The TEM image<br />
reported in Fig. 5 confirms the monodisperse <strong>nanoparticles</strong><br />
<strong>of</strong> LaFeO 3 with the particle sizes ranging<br />
from 20 to 50 nm.<br />
Table 1 reflects the specific <strong>surface</strong> <strong>area</strong>s <strong>of</strong> the<br />
LaFeO 3 prepared <strong>by</strong> the template method and the<br />
citrate method in our group (Li et al. 2007),<br />
respectively. By comparison, two main points can<br />
be found. One is that, at the same calcination<br />
temperature, the LaFeO 3 prepared <strong>by</strong> the template<br />
method has much <strong>large</strong>r <strong>surface</strong> <strong>area</strong> than that<br />
prepared via the citrate method and the other is that<br />
the <strong>surface</strong> <strong>area</strong> <strong>of</strong> the LaFeO 3 gradually decreases<br />
with increasing calcination temperature, which is<br />
mainly attributed to the increase in the particle size.<br />
However, compared with the LaFeO 3 prepared via<br />
the citrate method at the low temperature, the LaFeO 3<br />
Intensity (a.u.)<br />
900°C<br />
800°C<br />
700°C<br />
600°C<br />
500°C<br />
Absorbed volume (cm 3 / g)<br />
80<br />
60<br />
40<br />
20<br />
dV/dR (cm 3 g -1 nm -1 )<br />
0.002<br />
0.001<br />
0.000<br />
0 5 10 15 20 25 30<br />
Pore diameter (nm)<br />
20 30 40 50 60<br />
2θ (degree)<br />
Fig. 3 XRD patterns <strong>of</strong> LaFeO 3 samples calcined at different<br />
temperature<br />
0.0 0.2 0.4 0.6 0.8 1.0<br />
Relative pressure (p / p o<br />
)<br />
Fig. 4 N 2 adsorption–desorption isotherm for the templatefree<br />
LaFeO 3 calcined at 700 °C and pore size distributions<br />
calculated from desorption branch <strong>by</strong> the BJH method<br />
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J Nanopart Res<br />
Fig. 5 TEM image <strong>of</strong> LaFeO 3 calcined at 700 °C<br />
Table 1 BET <strong>surface</strong> <strong>area</strong> <strong>of</strong> the LaFeO 3 samples prepared<br />
<strong>by</strong> different methods<br />
Calcination<br />
temperature (°C)<br />
prepared <strong>by</strong> the template method still can have a high<br />
<strong>surface</strong> <strong>area</strong>, even after calcination at 900 °C. Based<br />
on the above analyses <strong>of</strong> the N 2 adsorption–desorption,<br />
BET, and TEM observation, it can be deduced<br />
that the disordered porous structure in the particles<br />
and the relative small particle size are responsible for<br />
the high <strong>surface</strong> <strong>area</strong> <strong>of</strong> the resulting LaFeO 3 .<br />
Measurement <strong>of</strong> XPS<br />
BET <strong>surface</strong> <strong>area</strong> (m 2 g -1 )<br />
By the template<br />
method<br />
500 – 15.0<br />
600 129.6 9.2<br />
700 101.1 6.3<br />
800 85.4 4.3<br />
900 34.5 3.2<br />
By the citrate<br />
method<br />
The XPS spectra <strong>of</strong> La3d, Fe2p, and O1s <strong>of</strong> the<br />
resulting LaFeO 3 after calcination at 700 and 800 °C<br />
were performed, as shown in Fig. 6. The binding<br />
energies obtained in the XPS analysis are standardized<br />
for specimen charging using C1s as the reference<br />
at 284.6 eV. The XPS peak positions <strong>of</strong> La3d 5/2<br />
(Fig. 6a) and Fe2p 3/2 (Fig. 6b) are at about 834.8 and<br />
710.5 eV, respectively, demonstrating that the main<br />
chemical valences <strong>of</strong> La and Fe in the two samples<br />
both are ?3 according to the method principle and<br />
handbook <strong>of</strong> the XPS instrument and the literature<br />
(Yang et al. 2006). The two O1s XPS spectra<br />
(Fig. 6c) are wide and asymmetric, demonstrating<br />
that there are at least two kinds <strong>of</strong> O chemical states<br />
according to the binding energy range from about<br />
526.0 to 534.0 eV, including crystal lattice oxygen<br />
(O L ) and hydroxyl oxygen (O H ) with increasing<br />
binding energy (Zhang et al. 2006; Jing et al. 2006).<br />
Thus, the O1s XPS spectrum is fitted to two kinds <strong>of</strong><br />
chemical states with the Origin s<strong>of</strong>tware <strong>by</strong> Gaussian<br />
rule. The O L XPS signal is attributed to the contribution<br />
<strong>of</strong> La–O and Fe–O in LaFeO 3 crystal lattice,<br />
and its peak position is at about 529.5 eV. The O H<br />
XPS is close related to the hydroxyl groups resulting<br />
mainly from the chemisorbed water, and its peak<br />
position is at about 531.5 eV. As seen from Fig. 6c,<br />
the amount <strong>of</strong> hydroxyl oxygen (O H ) decreases as the<br />
thermal treatment is enhanced.<br />
Measurements <strong>of</strong> UV–Vis DRS and SPS<br />
Figure 7 shows the UV–Vis DRS spectra <strong>of</strong> LaFeO 3<br />
samples calcined at different temperature; it can be seen<br />
that the DRS spectra <strong>of</strong> all LaFeO 3 samples are similar,<br />
and upon the calcination temperature increasing, the<br />
absorption <strong>of</strong> the spectra above 550 nm is decreased<br />
gradually, which is the cause that the LaFeO 3 crystallinity<br />
increases with the calcination temperature<br />
increasing on the basis <strong>of</strong> XRD measurement. According<br />
to the energy band structure <strong>of</strong> LaFeO 3 similar to<br />
that <strong>of</strong> a-Fe 2 O 3 (Lu et al. 2005), it can be concluded that<br />
the DRS spectra <strong>of</strong> LaFeO 3 <strong>nanoparticles</strong> are ascribed<br />
to the electronic transitions from the valence band to<br />
conduction band (O 2p ? Fe 3d ) (Li et al. 2000). In<br />
addition, it can be ascertained that the as-prepared<br />
LaFeO 3 samples can be excited <strong>by</strong> the light with the<br />
wavelength <strong>of</strong> equal to or smaller than 550 nm.<br />
The SPS technique can provide a rapid, nondestructive<br />
test <strong>of</strong> semiconductor solid <strong>surface</strong> property,<br />
and is also a very effective way to study the separation<br />
and transfer behavior <strong>of</strong> photoinduced charge carriers at<br />
a <strong>surface</strong> or interface (Jing et al. 2006). Figure 8 shows<br />
the SPS response <strong>of</strong> LaFeO 3 <strong>nanoparticles</strong> calcined at<br />
different temperature. It can be found that all <strong>of</strong> these<br />
samples display obvious SPS response in the<br />
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J Nanopart Res<br />
a<br />
La3d<br />
50<br />
Intensity (a.u.)<br />
800°C<br />
3d 5/2<br />
3d 3/2<br />
DRS (%)<br />
40<br />
30<br />
20<br />
10<br />
900°C<br />
800°C<br />
700°C<br />
600°C<br />
b<br />
Intensity (a.u.)<br />
Intensity (a.u.)<br />
820 830 840 850 860<br />
Binding energy (eV)<br />
c<br />
700°C<br />
800°C<br />
700°C<br />
2p 3/2<br />
2p 1/2<br />
700 710 720 730<br />
Binding energy (eV)<br />
800°C<br />
700°C<br />
524 528 532 536<br />
Binding energy (eV)<br />
Fe2p<br />
wavelength range from 300 to 550 nm, with a SPS peak<br />
at about 390 nm, which can be attributed to the<br />
photoinduced electronic transitions from the valence<br />
band to conduction band (O 2p ? Fe 3d ) (Li et al. 2000).<br />
O L<br />
O L<br />
O H<br />
O H<br />
O1s<br />
Fig. 6 XPS spectra <strong>of</strong> La3d (a), Fe2p (b), and O1s (c) <strong>of</strong><br />
LaFeO 3 samples calcined at 700 and 800 °C<br />
0<br />
300 350 400 450 500 550 600 650 700<br />
Wavelength (nm)<br />
Fig. 7 UV–Vis DRS spectra <strong>of</strong> LaFeO 3 samples calcined at<br />
different temperature<br />
Moreover, the SPS response becomes much stronger<br />
with increasing calcination temperature, which is close<br />
related to the increase in the crystallinity <strong>of</strong> the LaFeO 3 .<br />
The high crystallinity makes electronic band perfect so<br />
as to enhance the built-in field strength, which can<br />
promote charge separation, meanwhile leading to the<br />
decrease <strong>of</strong> the defect amounts, which is also favorable<br />
for charge separation (Jing et al. 2006). According to the<br />
SPS method principles, it can be expected that the<br />
stronger is the SPS signal, the higher is the photoinduced<br />
charge separation rate. Thus, it can be supposed<br />
that the high crystallinity is favorable for the photoinduced<br />
charge separation and then improve the photocatalytic<br />
activity further.<br />
Photocatalytic activity evaluation<br />
The activity <strong>of</strong> the as-prepared LaFeO 3 was evaluated<br />
<strong>by</strong> photocatalytic degradation <strong>of</strong> Rhodamine B solution<br />
under visible light. Figure 9 shows the RhB<br />
degradation rate <strong>of</strong> photocatalytic reaction under<br />
visible irradiation and adsorption in the dark on the<br />
different LaFeO 3 samples and internationally commercial<br />
P-25 TiO 2 . As the calcination temperature is<br />
enhanced, it can be noticed that the photocatalytic<br />
activity <strong>of</strong> the as-prepared LaFeO 3 gradually increases,<br />
and the LaFeO 3 calcined at 900 °C exhibits excellent<br />
photocatalytic activity. Interestingly, all the LaFeO 3<br />
samples display higher visible activity than P25 TiO 2<br />
and those LaFeO 3 samples prepared via the citrate<br />
method (Li et al. 2007). Based on the above discussion,<br />
the high photocatalytic activity is mainly explained<br />
from the following two aspects. One is the <strong>large</strong> <strong>surface</strong><br />
123
J Nanopart Res<br />
Photovoltage (a.u.)<br />
0.00008<br />
0.00006<br />
0.00004<br />
0.00002<br />
0.00000<br />
<strong>area</strong> <strong>of</strong> the as-prepared LaFeO 3 , which is favorable for<br />
the adsorption <strong>of</strong> RhB. This can be proved <strong>by</strong> the<br />
adsorption rate in Fig. 9, even still with a <strong>large</strong> RhB<br />
adsorption rate after calcination at 900 °C. The other is<br />
the high crystallinity <strong>of</strong> the as-prepared LaFeO 3 caused<br />
<strong>by</strong> calcined at the high temperature. The high crystallinity<br />
can promote the photoinduced charge separation<br />
(Jing et al. 2006). In addition, a certain amount <strong>of</strong><br />
<strong>surface</strong> hydroxyl group is also beneficial for photocatalytic<br />
reactions.<br />
Conclusions<br />
900°C<br />
800°C<br />
700°C<br />
600°C<br />
300 350 400 450 500 550 600<br />
Wavelength (nm)<br />
Fig. 8 SPS responses <strong>of</strong> LaFeO 3 samples calcined at different<br />
temperature<br />
On the basis <strong>of</strong> the above systematical investigations,<br />
the following conclusions can be drawn: (1) nanosized<br />
LaFeO 3 with <strong>large</strong> <strong>surface</strong> <strong>area</strong> has been<br />
successfully fabricated <strong>by</strong> using mesoporous silica<br />
<strong>SBA</strong>-<strong>16</strong> as hard template, still with 85 m 2 g -1<br />
<strong>surface</strong> <strong>area</strong> after calcination at 800 °C. At the same<br />
thermal treatment temperature, the <strong>surface</strong> <strong>area</strong> <strong>of</strong> the<br />
LaFeO 3 prepared <strong>by</strong> the template method is much<br />
<strong>large</strong>r than that prepared via the citrate method; (2)<br />
the as-prepared LaFeO 3 , especially for those calcined<br />
at high temperature, exhibits high visible activity; (3)<br />
the high activity <strong>of</strong> the as-prepared LaFeO 3 is<br />
attributed to the <strong>large</strong> <strong>surface</strong> <strong>area</strong> and high charge<br />
separation rate resulting from the high crystallinity,<br />
as well as to a certain amount <strong>of</strong> <strong>surface</strong> hydroxyl<br />
group. It can be suggested that the SPS method is an<br />
effective tool to reveal the processes <strong>of</strong> separation<br />
and transfer <strong>of</strong> photoinduced charges. This study<br />
provides a new route to design and synthesize other<br />
metal composite oxides with <strong>large</strong> <strong>surface</strong> <strong>area</strong>, and<br />
RhB degradation rate (%)<br />
50<br />
40<br />
30<br />
20<br />
10<br />
0<br />
would broaden the scope <strong>of</strong> the application <strong>of</strong><br />
perovskite-type materials.<br />
Actually, compared with porous TiO 2 and other<br />
oxide nano-materials routinely with hundreds <strong>of</strong><br />
meters squared per gram, the as-prepared nanosized<br />
LaFeO 3 has still low specific <strong>surface</strong> <strong>area</strong>. However,<br />
the superior visible photocatalytic performance <strong>of</strong><br />
this LaFeO 3 over international P25 TiO 2 is confirmed,<br />
implying that the porous perovskite-based<br />
nanomaterials, as non-TiO 2 -based visible-driven<br />
photocatalysts, are feasible and promising.<br />
Acknowledgments We gratefully acknowledge the fundings<br />
received from the National Nature Science Foundation <strong>of</strong><br />
China (No. 20501007, 20676027), the program for New<br />
Century Excellent Talents in universities (NCET-07-259), the<br />
Key project <strong>of</strong> Science & Technology Research <strong>of</strong> Ministry <strong>of</strong><br />
Education <strong>of</strong> China (No. 207027), the Science Foundation <strong>of</strong><br />
Excellent Youth <strong>of</strong> Heilongjiang Province <strong>of</strong> China<br />
(JC200701), and the Science Foundation <strong>of</strong> Harbin City <strong>of</strong><br />
China (No. 2005AFQXJ060), for the completion <strong>of</strong> this study.<br />
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Adsorption in the dark<br />
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