Morphological impact of ZnO nanoparticle on MEHPPV:ZnO based hybrid solar cell
-
Upload
partha-pratim -
Category
Documents
-
view
212 -
download
0
Transcript of Morphological impact of ZnO nanoparticle on MEHPPV:ZnO based hybrid solar cell
Morphological impact of ZnO nanoparticle on MEHPPV:ZnObased hybrid solar cell
Somnath Middya • Animesh Layek •
Arka Dey • Partha Pratim Ray
Received: 24 May 2013 / Accepted: 16 August 2013 / Published online: 28 August 2013
� Springer Science+Business Media New York 2013
Abstract In this study, we have synthesized semicon-
ducting ZnO nanoparticles (NP) of different morphology in
solvothermal route, by using different capping reagents and
applied it as an acceptor in poly(2-methoxy-5(2-ethyl-
hexyloxy)-phenylene-vinylene (MEHPPV):ZnO NP based
hybrid photovoltaic devices. Material properties of ZnO
NP of different morphology and the compositions were
studied with the help of X-ray diffraction, scanning elec-
tron microscopy, fourier transform infrared and thermo
gravimetric analysis. The direct band gap energies of
flower, sphere and rod-like ZnO NP were calculated as
3.68, 3.15 and 3.25 eV by using Tauc’s plot with the help
of UV–Vis absorption. We have studied different material
properties of MEHPPV:ZnO composite to check their
applicability as an active layer of hybrid solar cell. Photo-
luminescence (PL) spectra of the composite materials were
recorded to check PL energy quenching which is quite
noticeable in case of sphere-like nanoparticle. Finally the
hybrid solar cell of the structure ITO/PEDOT:PSS/ME-
HPPV:ZnO/Al has been fabricated and studied. From the
current density (J)–voltage (V) characteristic, we have
found that the solar cell fabricated with ZnO sphere-like
structure gives better result.
1 Introduction
In last few years there has been a tremendous effort to
develop inorganic semiconducting nanoparticles (NP) with
their application in organic–inorganic hybrid solar cells to
reduce the cost by optimizing the active material. Inorganic
NP incorporation within polymer matrix has been the
subject of considerable research because of their potential
for optical, electrical, and photovoltaic application [1, 2].
Recent investigations of promising materials for organic
light emitting diodes (OLEDs) and solar cell have dem-
onstrated that introduction of n-type inorganic NP into
conjugated polymers produce stable and high performance
devices [3]. Several inorganic NP were successfully
applied to develop solar cell [4]. Among the inorganic NP,
ZnO is a non toxic n-type wide bandgap semiconducting
material, which was applied efficiently in thin film tran-
sistors [5], light emitting diodes [6], optical sensors [7] and
in solar cells [8]. Since the band gap energy of ZnO NP is
wide, exciton binding energy is very high (60 meV) [9] and
optical transparency is also high [10], it was selected as one
of the promising material in fabrication of organic inor-
ganic hybrid solar cells [11]. The large excitonic binding
energy of ZnO leads to extreme stability of excitons at high
temperature [12] and enables the devices to work at low
threshold voltage. Another important property of ZnO NP
is the morphology dependant tunability of electron mobil-
ity [13]. So the nanomaterial with a suitable band gap for a
particular device application can be prepared by changing
their morphology. The absorption depends on the effective
surface area of the absorbing materials, which effectively
modifies the direct band gap. According to Burstein–Moss
effect, depending upon the morphological growth of
semiconducting NP and doping concentration [14, 15] the
absorption edge is pushed to higher energies because all
states close to the conduction band become populated. The
higher band gap material is superior in transition of exci-
tons above room temperature.
There had been a tremendous effort to synthesize
ZnO NP of different morphology. Flower-like, prism like,
S. Middya � A. Layek � A. Dey � P. P. Ray (&)
Department of Physics, Jadavpur University, Kolkata 700 032,
India
e-mail: [email protected]
123
J Mater Sci: Mater Electron (2013) 24:4621–4629
DOI 10.1007/s10854-013-1453-2
rod-like, snow-flakes like ZnO NP had been reported by
Zhang et. al. [16]. Gao et al. [17] prepared flower-like ZnO
by thermolysis technique. Yang et al. presented the syn-
thesis of flower-like, disk like and dumbbell like ZnO
structures with the assistance of capping molecules such as
citric acid and polyvinyl alcohol [18]. In this work we have
described the synthesis of flower-like, rod-like and sphere-
like ZnO NP by using solvothermal technique with various
capping reagents.
The main objective of this work is to study the effect of
incorporation of different nanostructured ZnO NP within
conducting unsaturated poly[2-methoxy-5-(2-ethyl-hexyl-
oxy)-1,4-phenylene-vinylene] (MEH-PPV) matrix. MEH-
PPV polymer has a high hole mobility but low electron
mobility [19] with HOMO level at -5.1 eV and LUMO
level at -2.7 eV. Imbalance in intrinsic carrier mobility
within MEH-PPV severely limits the performance of
polymer based solar cells. To overcome this imbalance,
ZnO can be selected as one of the semiconducting electron
acceptor with band gap 3.37 eV. The formation of exciton
and the charge transformation process from donor (MEH-
PPV) to acceptor (ZnO NP) has been schematically shown
in Fig. 1.
In this research work flower-like, sphere-like and rod-
like ZnO NP with different band gap and higher thermal
stability, were synthesized by solvothermal technique with
the help of poly (vinyl-pyrrolidone) (PVP), cetyl-trimethyl-
ammoniumbromide (CTAB) and tetra-octyl-ammonium-
bromide (TOAB) capping reagent. These ZnO NP with
different morphology have been incorporated within MEH-
PPV to prepare the active layer of hybrid solar cell. We
have characterized and studied the variation of absorption
of the polymer-NP composite material with effective sur-
face area of ZnO NP, due to the change in morphology.
The organic–inorganic hybrid solar cell, having structure
ITO/PEDOT:PSS/MEHPPV:ZnO(NP)/Al was fabricated
with synthesized nanoparticle of different morphology.
2 Experimental reagents
Dehydrated zinc-acetate (99 % pure), sodium hydroxide
pellet, TOAB, CTAB, PVP and Methanol of AR grade
were purchased from Merck, whereas MEH-PPV was
purchased from Sigma Aldrich. All these reagents were
used as precursor without further purification.
3 Experimental details
3.1 Synthesis of ZnO nanoparticles of different
morphology
ZnO NP of different morphology were synthesized by
using the procedure proposed by Bahnemann et al. [20] and
have also been adopted by various other groups [21]. In a
typical synthesis of surfactant-coated ZnO NP, in 20 ml
methanol, 1 mM (0.05 g) Zn (ac) 2:2H2O was dissolved by
vigorous stirring at about 50 �C and diluted to 200 ml
followed by cooling to room temperature. The solution was
then divided to three aliquot volumes, each of which was
taken in separate flask and were marked as (a), (b) and (c).
Specific surfactant TOAB, CTAB, PVP were added
respectively into the above pre-marked solutions under
vigorous stirring [22]. 0.02 M, 15 ml NaOH solution in
methanol was added drop-wise to each of the mixture
within few minutes under stirring. A white ppt was formed
in each case, which was found to be stable at ambient
conditions. Each ppt was then transferred to linear Teflon
autoclave and was heated at 160 �C for 2 days and was
cooled to room temperature. Thereafter the solutions were
washed with distilled water and ethanol repeatedly to
extract ZnO NP by centrifuged technique and were dried at
about 120 �C under vacuum heater.
In analytical measurements, X-ray diffraction (XRD) pat-
tern of ZnO NP were done with the help of Bruker D8 X-ray
diffractometer with CuKa radiation (k = 0.15418 nm). The
different ZnO nanoparticle morphological structures were
depicted by using scanning electron microscopy (SEM).
Thermogravimetric analysis of the materials was done with
the help of DTG-60 Thermogravimetric and differential
thermal analyzer of Shimadzu. Fourier transform infrared
(FTIR) spectra of ZnO were recorded with the help of FTIR-
8400S Spectrophotometer of Shimadzu. With FTIR Spec-
troscopic data, the occurrence of functional groups were
investigated. Optical absorption spectra were taken by spec-
trophotometer 2401PC from Shimadzu, whereas in fluores-
cence studies, the emission spectra were recorded on a VarianFig. 1 Schematics diagram of exciton dissociation and charge
transfer
4622 J Mater Sci: Mater Electron (2013) 24:4621–4629
123
Fluorescence Spectrophotometer of Carrier Eclipse. The
average particle size of each sample (lies between and
100 nm) was determined from XRD-spectra using scherrer’s
broadening equation. The direct band gap energies of syn-
thesized NP were measured with the help of Tauc’s plots from
UV–Vis absorption spectrum.
3.2 Fabrication and characterization of active materials
(MEHPPV:ZnO nanocomposite) and solar cell
To study the optical and electrical properties of the active
material, the solutions of MEH-PPV and ZnO NP of dif-
ferent morphology marked as (a), (b) and (c) were prepared
separately in chloroform with a concentration of 1.5, 0.3,
0.3 and 0.3 mg/mL respectively and were ultrasonicated
for 10 min at room temperature after stirring by magnetic
stirrer for 2 h each at open atmosphere. Once the solutions
were ready, MEH-PPV and ZnO nanoparticle were mixed
with appropriate wt. ratio 2:0.1 to get the desired composite
and was ultrasonicated for 30 min.
Prior to device fabrication, the ITO coated glass sub-
strates were cleaned with soap solution, acetone, ethanol
and distilled water by ultrasonication technique and were
dried under a vacuum oven. Before preparing the active
layer, a thin transparent buffer layer of PEDOT:PSS was
spin coated (at spin rate 1400 rpm for 2 min) on the
cleaned ITO coated glass substrate and was dried at 70 �C
under vacuum oven. As the substrate was ready, pre-pre-
pared active composite solutions of MEHPPV:ZnO (NP of
different morphology) were spin coated on the PE-
DOT:PSS film by spinning at the rate of 1200 rpm for
2 min. The desired film was obtained and dried under
vacuum desiccator at room temperature for 24 h. For the
top contact, aluminum electrode was deposited by thermal
evaporation with shadow mask. As the devices of structure
ITO/PEDOT:PSS/MEHPPV:ZnO/Al became ready, one
need to characterize it. The current density (J)–voltage
(V) characterizations of the respective cells were measured
with the help of Keithley 2400 source meter under the
incident illumination of white light (80 mWcm-2).
4 Results and discussions
4.1 SEM images and morphology
Figure 2a–c represent the SEM images of the synthesized
materials premarked as (a), (b) and (c) sequentially. The
images illustrate that morphology of the material (a),
(b) and (c) are flower-, sphere- and rod-like respectively
with their dimension in nano range. The architectural
growth of the nanoparticle eventually depends upon the
solubility of the precursor in the solvents with different
saturated vapor pressure and also upon the initial nucle-
ation of the crystals [23, 24]. The water soluble surfactant
(like TOAB, CTAB and PVP) can form a coordinate bond
with the Zn ions on growing particles [25]. The lower
vapor pressures set aside for rapid growth of the ZnO
nuclei. The chain length of the surfactant TOAB, CTAB
and PVP also effected the crystal growth accordingly. The
flower-like architecture was formed due to the coagulations
of ZnO flakes, which are formed due to uncontrolled
growth of materials. The ZnO nanorods have their different
orientations with hexagonal cross-section.
4.2 X-ray diffraction analysis
As synthesized ZnO NP of different morphology
[(a) flower-like, (b) sphere-like and (c) rod-like] were
characterized by powder XRD spectra, recorded with the
help of Bruker D8 X-ray diffractometer with copper (Cu)
as a target material. Figure 3a–c show the XRD spectra of
the flower-, sphere- and rod-like nanomaterials respec-
tively. The responsible Braggs diffractions were taken
place for the (hkl) planes (100), (002) and (101) were
identified at angle 2h = 32�, 34.6� and 36.4� respectively
Fig. 2 a SEM image of ZnO flower-like nanoparticle. b SEM image of ZnO sphere-like nanoparticle. c SEM image of ZnO rod-like nanoparticle
J Mater Sci: Mater Electron (2013) 24:4621–4629 4623
123
for each morphology, which indicate about the phase
identity. The XRD data approved ZnO, which were sup-
ported by the JCPDS Card No: 36-1451 [16]. Although
there was no significant change in diffraction pattern yet
change is found in relative intensity. For the (002) plane
the variation of intensity is quite noticeable. It may be due
to the orientation of responsible plane during crystal
growth. Using XRD data and applying Debye–Scherrer’s
broadening equation, the average particle size of the
(a) flower-like ZnO, (b) sphere-like ZnO and (c) rod-like
ZnO NP are calculated as 86, 26 and 57 nm respectively.
4.3 FTIR analysis
Figure 4a–c represent the fourier transformation infrared
spectroscopy (FTIR) of the synthesized ZnO NP of dif-
ferent morphology [(a) flower-, (b) sphere- and (c) rod-like
sequentially]. The spectra show strong peak around
3400–3430 cm-1 for O–H stretching and a small peak
around 2925–2920 cm-1 corresponding to C–H stretching
for each samples. Peaks around 1650–1500 and
1400–1370 cm-1 indicated the formation of ZnO [26] and
symmetric stretching of carboxylate group (COO–) which
probably comes from the un-reacted acetates. Peaks at
around 560 cm-1 show the distinct stretching vibration of
Zn–O. These functional groups exhibited solubility of the
NP in solvent.
(a)
(b)
(c)
Fig. 3 a XRD spectra of ZnO flower-like nanoparticle. b XRD
spectra of ZnO sphere-like nanoparticle. c XRD spectra of ZnO rod-
like nanoparticle
Fig. 4 Fourier transform Infrared spectra of a flower-like ZnO (black
in colour), b sphere-like ZnO (red in colour) and c rod-like ZnO
nanoparticles (blue in colour) (Color figure online)
4624 J Mater Sci: Mater Electron (2013) 24:4621–4629
123
4.4 UV–Vis absorption spectra and direct band gap
The absorption spectra of the ZnO NP (of (a) flower-like,
(b) sphere-like and (c) rod-like) in chloroform medium
were recorded in the wavelength range of 300–600 nm.
From these spectra, given in inset of Fig. 5a–c respectively
clearly illustrated that the (b) sphere-like nanoparticle
absorbs comparably larger part of the incident radiations in
comparison with (a) flower-like and (c) rod-like ZnO NP.
Considering the absorption data, with the help of Tauc’s
equation direct band gap of the samples were measured as
3.68, 3.15 and 3.25 eV respectively (plots are given in
Fig. 5a–c) for flower-, sphere- and rod-like morphology.
The band gap of ZnO nanoparticle is 3.3 eV, as reported
earlier in the literature by Berger et al. 1997 [27] and
3.4 eV, reported by Samuel et.al. [28]. Since the band gap
of flower-like structure is comparably high, its absorbance
is low. But the absorption is quite high in case of sphere-
like nano morphology, due to its lower band gap. For
photovoltaic application in higher temperature (from room
temperature), inorganic semiconductor with wide band gap
has more significant role. The direct band gap energy was
significantly changed in case of sphere and rod-like struc-
ture of ZnO, depending upon their morphological changes.
It may be due to the increased populations of all states
close to the conduction band. Hence one can say that
sphere-like structure is more suitable in high temperature
application of hybrid solar cells with organic polymer.
4.5 Thermo-gravimetric analysis
DTG-60 thermogravimetric and differential thermal ana-
lyzer of Shimadzu was used to study the thermal stability
of ZnO NP. Approximately 5 mg of the samples were
heated to 600 �C at the rate of 10 �C/min. From Fig. 6, it is
observed that TGA curves for the nano ZnO of different
morphology show no drastic loss in weight. This indicates
the thermal stability and high purity of nano ZnO. The
TGA curves corresponding to the (a) flower-like,
(b) sphere-like and (c) rod-like ZnO samples show a very
small decrease in weight percentage at around 190–250 �C.
As reported by Morishige et al. [29] the change at around
200 �C may be seen due to the decomposition of the
condensation dehydration of the hydroxyls. As the tem-
perature was increased, the decomposition starts gradually
and results in weight lost. The rate of decomposition is
quite high in case of ZnO (a) flower-like NP (represented
as (a) in graph), and at temperature 600 �C it is decom-
posed to 65 % of its initial weight. Whereas in case of
(c) rod-like (represented as (c) in graph) and (c) sphere-like
ZnO (represented as (b) in graph), weight was degraded to
75 and 72 % respectively. From the curves it is clearly
demonstrated that the (c) rod-like and (b) sphere-like ZnO
Fig. 5 a Tauc’s plot of ZnO flower-like nanoparticles. b Tauc’s plot
of ZnO sphere-like nanoparticles. c Tauc’s plot of ZnO rod-like
nanoparticles
J Mater Sci: Mater Electron (2013) 24:4621–4629 4625
123
NP are thermally more stable in comparison with flower-
like ZnO one.
4.6 UV–Vis absorption and band gap of MEHPPV
To optimize the photo sensing behavior of MEH-PPV,
UV–Vis absorption spectra in the range of 300–700 nm
was recorded with the help of spectrophotometer (given in
Fig. 7). From these spectra the most excitation wavelength
558 nm for MEH-PPV was observed and hence corre-
sponding band gap energy was calculated as 2.22 eV. [30].
Fig. 6 Thermogravimetric (TG) plots of a flower-like ZnO, b sphere-
like ZnO and c rod-like ZnO nanomaterials
Fig. 7 UV–Vis absorption spectra of MEH-PPV polymer in chloro-
form medium
(a)
(b)
(c)
Fig. 8 a UV–Vis absorption spectra of MEH-PPV polymer, ZnO
flower-like NP and MEHPPV:ZnO composite in chloroform medium.
b UV–Vis absorption spectra of MEH-PPV polymer, ZnO sphere-like
NP and MEHPPV:ZnO composite in chloroform medium. c UV-Vis
absorption spectra of MEH-PPV polymer, ZnO rod-like NP and
MEHPPV:ZnO composite in chloroform medium
4626 J Mater Sci: Mater Electron (2013) 24:4621–4629
123
Lee et.al. [31] reported the band gap energy of MEH-PPV
as 2.1 eV by optimizing HOMO and LUMO energy levels.
4.7 UV–Vis absorption analysis for the organic–
inorganic composites
Figure 8a–c represent the UV–Vis absorption spectra of
MEH-PPV, ZnO and MEHPPV:ZnO composite with dif-
ferent morphology in chloroform medium. From these
spectra it is clear that the absorption of MEH-PPV
increased due to incorporation of inorganic ZnO nanopar-
ticle. The spectrum of the composite represents the
superposed spectra of donor (MEH-PPV) and acceptor
(ZnO) material. Red shift of the resultant spectrum is
observed due to incorporation of inorganic nano material
within MEH-PPV.
4.8 Photo-luminescence and energy quenching
Figure 9 represents the photoluminescence spectra of
donor polymer MEH-PPV and MEH-PPV with ZnO
nanoparticle in chloroform medium, as recorded in the
wavelength range of 450–750 nm. In this figure, the photo-
luminescence (PL) peaks of MEH-PPV in chloroform
medium are observed around 583 and 638 nm. The PL
intensities are significantly reduced from the value of
MEH-PPV during formation of composite with ZnO
nanoparticle. In these spectra the static energy quenching
of MEH-PPV with incorporation of ZnO nanoparticle was
observed distinctly. The PL quenching is the evidence for
exciton dissociation. As the photogenerated excitons are
dissociated, the probability for recombination should be
significantly reduced. This is the ultrafast electron transfer
phenomena from donor to acceptor and it is expected to
increase the exciton dissociation efficiency in photovoltaic
devices [32]. In this composite, ZnO semiconducting
nanoparticle acts as acceptor material.
4.9 Current–voltage characteristic of solar cells
The J–V characteristics of the devices ITO/PEDOT:PSS/
MEHPPV:ZnO flower-like NP/Al, ITO/PEDOT:PSS/ME-
HPPV:ZnO sphere-like NP/Al and ITO/PEDOT:PSS/ME-
HPPV:ZnO rod-like NP/Al were measured with the help of
Keithley 2400 source meter, interfaced with PC. Figure 10
represents the J–V characteristic curves of each device. The
effective surface area of the active device that was fabri-
cated by masking is taken as 7.065 9 10-2 cm2. From
these J–V characteristic curves, the open circuit voltage
(VOC) and short circuit current density (JSC) were measured
as given in Table 1. The corresponding efficiency (g) as
well as fill factor (FF) of the devices was measured as 0.40,
0.55, 0.45 % and 0.51, 0.51, 0.58. In this investigation,
these characteristic curves demonstrate that the Jsc of the
device is improved for the ZnO sphere-like nano acceptor
materials. In organic–inorganic hybrid solar cell several
factors affect the performance of solar cell. Depending
upon the surface morphology and sphere-like symmetry of
ZnO nanoparticle, absorption ability of the conjugated
materials with MEH-PPV improved, which could increase
the generation rate of excitons. Moreover, the bulk resis-
tance that was developed due to the thickness of the film,
somehow controlled by morphology, was assume to be
reduced, as the sphere-like ZnO was incorporated within
MEH-PPV. ZnO rod-like structure was supposed to give
Fig. 9 Photo-luminescence spectra of MEH-PPV and MEHPPV:ZnO
composites with different morphology in chloroform medium
Fig. 10 Current density–voltage characteristics of a ITO/PE-
DOT:PSS/MEHPPV:ZnO (flower-like)/Al device, b ITO/PE-
DOT:PSS/MEHPPV:ZnO (sphere-like)/Al device, and c ITO/
PEDOT:PSS/MEHPPV:ZnO (rod-like)/Al device
J Mater Sci: Mater Electron (2013) 24:4621–4629 4627
123
better transport property for their architecture. But from the
J–V characteristic, the measured Jsc approved the contra-
dictory one, which rose due to the random direction of
alignment of nano rods. Performance of solar cell mostly
depends on the successive interfacing and energy quench-
ing between donor-acceptor materials, which mostly rela-
ted with the band gap energy and the absorption power of
the nano-inorganic materials. The energy quenching is
crudely related with the position of energy band spectra of
donor and acceptor materials. There is another possible
way to improve VOC by modifying the band gap of the
inorganic acceptor material, specifically by changing the
position of LUMO energy level, which can only be pos-
sible by controlling the growth of crystal during synthesis.
Since according to Shockley and Queisser [33], VOC is
directly related with the energy difference between LUMO
of acceptor and HOMO of donor material. The band gap
energy of flower-like morphology was increased in com-
parison to rod-like structure, as obtained from Tauc’s
equation. This increment in band gap energy demonstrated
with Burstein–Moss theory. Depending upon the morpho-
logical growth of semiconducting NP [34, 35], the
absorption edge is pushed to higher energies because all
states close to the conduction band become populated.
Hence the difference between LUMO energy level of
flower-like ZnO and HOMO energy level of MEH-PPV
approved the increment of Voc in comparison to the device
fabricated with rod-like nanoparticle in conjunction with
MEH-PPV. The formation of successive heterojunction
between organic donor and inorganic acceptor influences
upon the current density, depending upon the homogeneity
of the composite materials. This homogeneity is mostly
impacted by the dispersity of the inorganic nano particles
with their morphological identity and the occurrence of
functional groups. In this study the sphere-like morphology
was highly dispersed in chloroform with no detectable
agitation, in comparison to the rest synthesized materials,
which has been confirmed by the sharp and intense FTIR
spectra. Thus it had highest possibility to fabricate suc-
cessive hetero-junction with donor polymer in solution
phase as well as in thin film, as it had performed. PL
spectra exhibited the successive static energy quenching,
which approved the better charge transportation for ME-
HPPV:ZnO sphere-like composite [36–38]. It is important
to note that the higher series resistance reduces the FF. The
improved FF for the device fabricated with rod-like ZnO
NP exhibited the lower resistance of the film in comparison
to the device fabricated with flower-like ZnO. In this
experimental study, VOC as well as efficiency has been
improved for the device fabricated with sphere-like ZnO
nano semiconducting acceptor because of its lower bulk
resistance that may be occurred depending upon the mor-
phology. Thus there is every possibility to improve VOC.
Whereas, the VOC and the efficiency of the device, fabri-
cated with flower-like ZnO, improved in comparison with
the device, fabricated with rod-like ZnO nano material, due
to its higher absorption with lower band gap.
5 Conclusions
ZnO nano semiconducting material of different morphol-
ogy (flower-like, sphere-like and rod-like) were synthe-
sized successively in solvothermal technique by using
different capping reagents. Among these the sphere-like
one is more superior architecture with nano dimension and
better absorbing property. We have investigated the opti-
cal, thermal and electrical properties of all these synthe-
sized materials with conscience. The organic–inorganic
based solar cell, configured with MEH-PPV:ZnO sphere-
like morphology gives the highest efficiency with
improved Jsc and Voc. This is only because the formation of
successive junctions in between organic–inorganic com-
posite, which occur depending upon the structural sym-
metry with small particle size of sphere-like ZnO and its
high absorption with lower band gap energy.
Acknowledgments This work was supported by Department of
Science and Technology, Govt. of West Bengal under project No.
280(Sanc.)/ST/P/S&T/4G-10/2009.
References
1. W.U. Huynh, J.J. Dittmer, A.P. Alivisatos, Science 295, 2425
(2002)
2. A. Petrella, M. Tamborra, M.L. Curri et al., J Phys Chem B 109,
1554 (2005)
3. C. Kligshirn, Phys Status Solidi B 71, 547 (1975)
4. S.H. Yang, P.L. Rendu, T.P. Nguyen, C.S. Hsu, Rev Adv Mater
Sci 15, 144 (2007)
5. C.X. Ji, P.C. Searson, J Phys Chem B 107, 4494 (2003)
Table 1 characteristic parameters of the devices
Sample VOC
(Volt)
JSC
(mAcm-2)
Vmax
(Volt)
Jmax
(mAcm-2)
FF Efficiency (%)
ITO/PEDOT:PSS/MEHPPV:ZnO(a)/Al 0.555 1.131 0.357 0.899 0.51 0.40
ITO/PEDOT:PSS/MEHPPV:ZnO(b)/Al 0.587 1.461 0.408 1.081 0.51 0.55
ITO/PEDOT:PSS/MEHPPV:ZnO(c)/Al 0.508 1.222 0.299 1.197 0.58 0.45
4628 J Mater Sci: Mater Electron (2013) 24:4621–4629
123
6. N. Saito, H. Haneda, T. Sekiguchi, N. Ohashi, I. Sakaguchi, K.
Koumoto, Adv Mater 14, 418 (2002)
7. S.P. Singh, S.K. Arya, P. Pandey, B.D. Malhotra, S. Saha, K.
Sreenivas, V. Gupta, Appl Phys Lett 91, 063901 (2007)
8. F. Li, Y. Du, Y. Chen, L. Chen, J. Zhao, P. Wang, Sol Energy
Mater Sol Cell 97, 64 (2012)
9. V.A.L. Roy, A.B. Djurisic, W.K. Chan, J. Cao, H.F. Lui, C.
Surya, Appl Phys Lett 83, 141 (2003)
10. Q.H. Chen, W.G. Zhang, J Non-Cryst Solids 353, 374 (2007)
11. S.V. Bhat, A. Govindaraj, C.N.R. Rao, Sol Energy Mater Sol Cell
95, 2318 (2011)
12. Y. Chen, D.M. Bagnall, H. Koh, K. Park, K. Hiraga, Z. Zhu, T.
Yao, J Appl Phys 84, 3912 (1998)
13. C. Ton-That, M.R. Philips, T.P. Nguyen, J Lumin 128, 2031
(2008)
14. Y. Abdollahi, A.H. Abdullah, Z. Zainal, N.A. Yusof, Int J Basic
Appl Sci 11, 62 (2011)
15. P. Chakraborty, G. Datta, K. Ghatak, Phys Scr 68, 368 (2003)
16. J. Zhang et al., Chem Mater 14, 4172 (2002)
17. X. Gao, X. Li, W. Yu, J Solid State Chem 178, 1139
(2005)
18. H. Zhang, D. Yang, D. Li, X. Ma, S. Li, D. Que, Cryst Growth
Des 5, 547 (2005)
19. T. Sakanoue, E. Fujiwara, R. Yamada, H. Tada, Appl Phys Lett
84, 3037 (2004)
20. D.W. Bahnemann, C. Karmann, M.R. Hoffmann, J Phys Chem
91, 3789 (1987)
21. L. Guo, S. Yang, C. Yang, P. Yu, J. Wang, W. Ge, G.K.L. Wong,
Chem Mater 12, 2268 (2000)
22. M.L. Singla et al., J Lumin 129, 434 (2009)
23. S. Biswas, S. Kar, S. Chaudhuri, Mater Sci Eng B 142, 69 (2007)
24. N. Talebian, S.M. Amininezhad, M. Doudi, J Photochem Pho-
tobiol B 120, 66 (2013)
25. S. Lee, S. Jeong, D. Kim, S. Hwang, M. Jeon, J. Moon, Super-
lattices Microstruct 43, 330 (2008)
26. G.V. Seguel, B.L. Rivas, C. Novas, J Chil Chem Soc 50, 401
(2005)
27. L.I. Berger, Semiconductor materials (CRC Press, Boca Raton,
FL, 1997), pp. 198–203
28. M.S. Samuel, L. Bose, K.C. George, Acad Rev 16, 57 (2009)
29. K. Morishige, S. Kittaka, T. Moriyasu, J Chem Soc Faraday 176,
728 (1980)
30. N.Z. Yahya, M. Rusop, J Nanomater 793679, 4 (2012). doi:10.
1155/2012/793679
31. Y.Z. Lee, X. Chen, S.A. Chen, P.K. Wei, W.S. Fann, J Am Chem
Soc 123, 2296 (2001)
32. Y. Kang, D. Kim, Sol Energy Mater Sol Cells 90, 166 (2006)
33. W. Shockley, H. Queisser, J Appl Phys 32, 510 (1961)
34. Y. Abdollahi, A.H. Abdullah, Z. Zainal, N.A. Yusof, Int J Basic
Appl Sci 11(04), 62 (2011)
35. P. Chakraborty, G. Datta, K. Ghatak, Phys Scr 68, 368 (2003)
36. G. Yu, A.J. Heeger, J Appl Phys 78, 4510 (1995)
37. J. Yu, D. Hu, P.F. Barbara, Science 289, 1327 (2000)
38. Y. Kang, D. Kim, Scl Energy Mater Sol Cells 90, 166 (2006)
J Mater Sci: Mater Electron (2013) 24:4621–4629 4629
123