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Nano Res
1
Flexible organic-inorganic hybrid photodetectors with
n-type PCBM and p-type pearl-like GaP nanowires
Gui Chen,† Xuming Xie,
† and Guozhen Shen ()
Nano Res., Just Accepted Manuscript • DOI: 10.1007/s12274-014-0537-5
http://www.thenanoresearch.com on July 7, 2014
© Tsinghua University Press 2014
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Nano Research
DOI 10.1007/s12274-014-0537-5
Flexible organic-inorganic hybrid photodetectors with
n-type PCBM and p-type pearl-like GaP nanowires
Gui Chen, Xuming Xie, and Guozhen Shen*
Institute of Semiconductors, Chinese Academy of
Sciences, China
Flexible organic-inorganic hybrid photodetectors were
fabricated on various flexible substrates for the first time with
n-type PCBM and p-type pearl-like GaP nanowires, which
exhibited high mechanical flexibility, good folding strength,
excellent electrical stability and fast response.
Guozhen Shen, http://nanolab.tap.cn
Flexible organic-inorganic hybrid photodetectors with
n-type PCBM and p-type pearl-like GaP nanowires
Gui Chen,† Xuming Xie,† and Guozhen Shen ()
† G. Chen and X. Xie are visiting students from Huazhong University of Science and Technology. They contribute equally to this
work.
Received: day month year
Revised: day month year
Accepted: day month year
(automatically inserted by
the publisher)
© Tsinghua University Press
and Springer-Verlag Berlin
Heidelberg 2014
KEYWORDS
Nanowires; flexible;
photodetectors; hybrid
ABSTRACT
Flexible photodetectors have become one of the focuses of current researches
becaused of they may fit for some unique applications in various new areas that
require flexible, lightweight, and mechanical shock-resistive sensing elements.
In this work, we designed flexible organic-inorganic hybrid photodetectors on
various flexible substrates, including PET, common sellotape and PDMS, with
n-type PCBM and p-type pearl-like GaP nanowires (NWs) as the active
materials. The as-fabricated hybrid devices exhibited optimized performance
with a fast response time (43 ms) and high on/off ratio (~170) compared with
the device made of pristine GaP NWs. Under different bending condition, the
flexible hybrid photodetectors demonstrated excellent flexibility and electrical
stability, which are very promising for further large-scale, high sensitivity and
high speed photodetector applications.
1 Introduction
Photoresponse is a general property of
semiconductors and photodetection is of great
importance for various applications including
environmental and biological research, sensing,
detection and missile launch. Many kinds of
photodetectors with response to either deep UV light,
visible light, infrared light or broad wavelength
lights have been designed and demonstrated [1-5].
Recently, the use of hybrid nanostructures in
photodetectors has been an emerging research topic
due to their high surface-to-volume ratio, as well as
more freedom in the rational design of material
properties [6-9]. Heterostructures formed between
inorganic and organic materials could lead to many
unique device applications due to their unique
physical properties, such as mechanical flexibility,
large area, low temperature processability and high
performance. These hybrid materials demonstrated
not only the merits of organic polymer and inorganic
semiconductor, but also the advantage of the
interfaces between the components for the
transmission of electrons and holes [6-9]. Among the
investigated hybrid nanostructures, one-dimensional
(1-D) organic-inorganic hybrid nanostructures have
been widely investigated very recently as they
usually demonstrated excellent photovoltaic
behavior, rectification, light-emitting behavior and
photoresponse properties [10-14]. Photodetectors
built on these hybrid materials usually exhibited
superb photoresponse to light irradiation.
Nano Research
DOI (automatically inserted by the publisher)
Address correspondence to [email protected].
Research Article
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2 Nano Res.
Flexible electronics, referring to the technology that
integrates electronic/optoelectronic devices on
flexible substrates, have gained extensive attention
because of the attractive properties of flexible devices
such as biocompatibility, flexibility, light weight,
shock resistance, softness and transparency, as well
as the potential applications in future wearable
devices, paper displays, sensors and detectors,
energy conversion and storage devices.
In this work, by utilizing n-type
phenyl-C61-butyric acid methyl ester (PCBM) and
p-type GaP NWs as the sensing materials, we
designed high-performance flexible hybrid
photodetectors on various flexible substrates.
Pearl-like GaP NWs were first grown via a simple
chemical vapor deposition (CVD) method and their
electric transport and photoresponse properties were
investigated by fabricating single NW devices. By dip
coating mixed GaP:PCBM solution on flexible
substrates, including PET, common sellotape and
PDMS, highly flexible photodetectors were then
fabricated, which demonstrated optimized
performance with fast response time (43 ms) and
high on/off ratio (~170) compared with the device
made of pristine GaP NWs.
2 Experiments
2.1 Synthesis and Characterization of pearl-like
GaP nanowires
Pear-like GaP NWs were synthesized in a horizontal
tube furnace through a CVD process. In a typical
process, GaP power (Alfa Aesar, 99.999% purity),
serving as the source material, was loaded into an
alumina boat and positioned at the center of the tube.
Silicon wafers (100) were placed downstream, about
15 cm away from the GaP power to collect the
deposited products. Prior to heating, the reaction
system was purged with high-purity N2 for 1 h in
order to eliminate the remaining oxygen in the tube.
The furnace was heated from the room temperature
to 1000 oC in 30 min and kept at this temperature for
2 h. During the experimental process, a high-purity
N2 flow of 100 sccm was introduced into the reaction
system. After the reaction, the furnace was cooled to
room temperature and a layer of yellow wool-like
product was found on the Si substrate. The
as-synthesized product was characterized by X-ray
diffraction (XRD, X’pert Pro, PANalytical B.V.,
Netherlands), scanning electron microscopy (SEM,
Hitachi S4800) and transmission electron microscopy
(TEM, JEOL JEM-3000F) equipped with an
energy-dispersive X-ray spectrometer (EDS).
Photoluminescence (PL) spectrum was collected at
room temperature with an HORIBA Jobin Yvon
LabRAM Spectrometer HR 800 UV with a He-Cd
laser line at 514 nm as the excitation source.
2.2 Fabrication of field-effect transistors (FETs) and
hybrid photodetectors
Individual pearl-like GaP NW devices were
fabricated according to our previous reported
technique [15]. Briefly, the GaP NWs were first
dispersed in isopropanol and then dropped on a
thermally oxidized Si substrate covered with a 300
nm SiO2 layer. After the wafer was dried in air, UV
lithography, thermal evaporation and lift-off
processes were carried out to pattern the Cr/Au drain
and source electrodes (10 nm/100 nm) on both ends
of the NWs. PCBM (60 mg) was first dissolved in 4
mL of chloroform. A GaP NWs solution (100 μL,
about 80 mg mL-1) and a solution of PCBM (200 μL)
were mixed to from the final solution. To fabricate
the rigid photodetector, the mixed solution with
PCBM and GaP NWs was first dropped on a SiO2
(300 nm)/Si wafer and formed a hybrid film. Parallel
silver wires with an interval of 1 mm were fixed on
the film with silver paste as the binder. Then, the
devices were heated at 100 oC in a vacuum for 2 h to
solidify the silver paste. Similarly, the pure pearl-like
GaP NWs photodetectors on rigid SiO2/Si wafer were
fabricated. Meanwhile, the flexible photodetectors
can be also constructed on the flexible substrate (PET,
common sellotape and PDMS) by using a similar
process for the rigid device.
2.3 Electrical transport and photoresponse
measurements
The electrical transport measurements of single GaP
NW devices were conducted by the four-probe
station with a semiconductor characterization system
(Keithley 4200-SCS). The incident power of the light
was measured by an Ophir NOVA power meter.
Monochromatic light from a source composed of a
tungsten lamp (300 W) and a monochromator
(WDG15-Z) was focused and guided onto the
semiconductor NW. All measurements were
performed in air and at room temperature.
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3 Nano Res.
3 Results and discussion
The representative morphology of the product was
characterized by a SEM and the coresponding SEM
images were shown in Figure 1a-b. Figure 1a shows
the low-magnification SEM image of the product,
which reveals that the products are mainly composed
of pearl-like NWs with length ranging from several
to several tens of micrometers. The yield of the
pearl-like nanostructures is estimated to be about
90%. Figure 1b shows the high-magnification SEM
image of the as-grown product. It can be seen that,
for a single pearl-like NW, the diameter of the bulb
parts is in the range of 100-400 nm, and the diameter
of the trunk is about 150 nm.
The crystal structure of the as-synthesized product
was characterized by X-ray diffraction (XRD), as
shown in Figure. S1. All diffraction peaks can be
indexed to pure zinc blende (cubic) GaP (JCPDS No.
32-0397). No peaks from Ga2O3 or other crystalline
phase were detected, indicating the formation of
pure GaP phases. Figure 1c shows a typical PL
spectrum of the as-synthesized GaP product. Only a
sharp peak is observed and located in ~548 nm,
corresponding to the band-gap emission of GaP
(Eg=2.26 eV), which is in consistent with the literature
value [16].
Figure 1. (a-b) low-magnification and high-magnification SEM images, (c) PL spectrum, and (d) TEM image of the as-grown
GaP product. (e,f)HRTEM images of the corresponding parts shown in 1e and 1f. The inset in (f) shows the corresponding
SAED pattern of the as-prepared GaP NW.
To further get information about the detailed
microstructure of the pearl-like GaP nanowires, TEM
characterization was performed and the
corresponding results were shown in Figures 1d-f.
Figure 1d depicts a low-magnification TEM image of
a single GaP NW, which clearly revealed that the NW
is actually made of a straight nanowire (trunk park)
wrapped periodically with olive-shaped bulbs along
the whole trunk. The trunk NW has a diameter of
~150 nm, whereas the maximum diameter of the
bulbs is about 380 nm. The corresponding
high-resolution TEM (HRTEM) images from different
regions of the NW are shown in Figures 1e-f. Figure
1e is a lattice resolved HRTEM image taken from the
bulb part. The marked adjacent plane spacings are
both 0.315 nm, corresponding to the (111) lattice
planes of cubic GaP phase. A selected-area electron
diffraction (SAED) pattern and a HRTEM image
taken from the trunk part are shown in Figure 1f. As
can be seen, the spacings between two adjacent plane
have the same value of ~0.315 nm, which is also
assigned to the (111) lattice plane of cubic GaP
structure. The result indicated that the trunk NW has
preferred grown direction along the [111] orientation.
A SAED pattern of the trunk part is shown in the
inset, which further verifies its single crystal nature.
The corresponding EDS spectrums of both the
wrapped bulb part and the trunk part are depicted in
Figure S2a-b, respectively. From the curves, it can be
seen clearly that both parts are composed of only Ga
and P elements with a composition of ca. 1:1, close to
the stoichiometry of GaP. In the spectrum, signals
from C and Cu elements are from the TEM grid. And
the signal from O element (the inset in Figure. S2a)
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4 Nano Res.
may be from the surface oxide layers. On the basis of
the above elemental analysis, the products are
actually pearl-like GaP NWs composed of GaP trunk
NWs decorated with GaP bulbs.
Figure 2. (a) Ids-Vds curves at various Vgs, (b) Ids-Vgs curve measured at Vds=10V of single GaP NW based back-gate FET. The
inset is the SEM image of the device with a channel length of about 3 µm. (c) I-V curves and (d) reproducible on/off
switching (blue curve) of the hybrid PCBM :GaP film based device on Si/SiO2 substrate. The reproducible on/off switching
of pure GaP film was also shown (red curve).
Since the growth of the GaP NWs is via a one-step
process without the use of catalyst, the growth can be
proposed to be governed by a self-organization
vapor-solid (VS) process according to previous report
[17]. The whole growth process can be clearly
expressed in Figure S3. At high reaction temperature,
the mixed Ga and P vapor can be obtained by the
decomposition of GaP power and transferred by the
carrier high-purity N2 gas to a low-temperature
region. And they aggregate and deposit on the
surface of the Si wafer as a nuclei to form a trunk
nanowire. Meanwhile, the Ga vapor has a faster
transfer speed to the low-temperature region under a
high reaction temperature and form a viscous liquid
because of its lower melting point (29.8 oC).
Afterwards it reacts with the P vapor to form GaP
nanoparticles due to surface tension and deposit on
the surface of the firstly formed GaP NW [18-20].
With the increase of reaction time, the pearl-like GaP
NWs are formed.
In order to investigate the electronic transport
properties of the as-grown pearl-like GaP NWs,
single NW based FETs were first fabricated with the
common back-gate configuration on 300 nm
SiO2-coated Si wafer via a traditional lithography
process. The parallel Cr/Au (10/100 nm) films were
used as the source/drain electrodes and deposited on
both ends of the NWs. The inset in Figure 2a depicts
a SEM image of a single GaP device. A single
pearl-like GaP NW was observed to be pinned under
two Cr/Au electrodes. The channel width of the
device is about 3 μm. Figure 2a shows the drain
current (Ids) versus source-drain voltage (Vds) curves
of the device measured at different gate voltages (Vgs,
from -10 to 10 V). It can be seen clearly that the
conductance of the pearl-like GaP NW gradually
increases with decreased gate voltages ranging from
-10 to 10 V, indicating a typical p-type
semiconducting behaviour. The drain current (Ids)
versus gate voltage (Vgs) curves of the device was
also measured for the same device at a drain bias of
10 V and the result was shown in Figure 2b. At the
identical voltage, the drain current decreased when
the gate voltage varied from -10 V to 10 V, further
revealing that the pearl-like GaP NWs are typical
p-type semiconductors. Meanwhile, the threshold
voltage (Vth) of 3.4 V and On/Off ratio of ~102 can be
determined by extrapolating the linear regain of the
Ids-Vgs curve in Figure. 2b.
Recently, considerable attention has been focused
on organic-inorganic hybrid photodetectors due to
the fact that they can combine the merits of organic
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5 Nano Res.
semiconductor, such as large scale production
process with low cost, easily-tunable functionality
and the exceptional mechanical flexibility, and that of
the inorganic material, including superior intrinsic
carrier mobilities and broad spectrum absorption
capability. Therefore, hybridizing organic and
inorganic materials may lead to high performance
devices with versatile functions and excellent
flexibility [6,7,10,21]. In order to fabricate hybrid
organic/inorganic photodetectors, the pearl-like GaP
NWs were first mixed with PCBM to form a hybrid
film on a SiO2/Si wafer. Parallel silver electrodes with
an interval of 1 mm were then deposited on the film
to construct a prototype device. Figure 2c shows the
I-V curves of the hybrid device in dark and under
illumination with 550 nm light of different intensities.
It can be conspicuously observed that, at the same
voltage, the photocurrent increases gradually with
the increased light intensities, which can be
attributed to change in the photon intensity of the
hybrid organic-inorganic devices. Light can be
absorbed through the whole thickness of the device
and that of both types of charge carrier run within
the device. The light intensity dependence of the
photocurrent measured at a bias of 2 V is depicted in
Figure S4. The corresponding dependence of the
photodetector on light intensity can be fitted to a
power law, I =APθ [22,23]. By fitting the measured
data in the curve, the corresponding function is I~P0.77,
revealing that the photocurrent exhibits good
dependence on light intensity, which further
indicates the superior photocurrent capability of the
hybrid photodetector.
The high photosensitivity of the hybrid device
based on PCBM:GaP pearl-like NW hybrid film is
further confirmed by photocurrent measurements on
the device at the on/off states by periodically turning
on and off 550 nm light with a power intensity of 3.15
mW/cm2 at a bias of 2 V, as shown in Figure 2d. From
the curves, the photocurrent increases rapidly and
reaches steady state at the “ON” state upon light
illumination, and then decreased quickly to the
“OFF” state after the light was turned off, suggesting
the excellent stability and reproducibility of the
hybrid device. For the hybrid device, the current was
only 2.2 nA in the dark. However, the current could
approach 374 nA at an incident light intensity of 3.15
mW/cm2 and a bias voltage of 2.0 V. The on/off
switching ratio is about 170. Meanwhile, the rise time
of the hybrid device is about 43ms (shown in Figure
S4b). In contrast, devices based on pure GaP
pearl-like NWs showed quite low photocurrent of
228 nA at a bias voltage of 2.0 V, an enhancement of
about 40 times compared with its dark current of 5.7
nA. Meanwhile, the dark current (2.2 nA) in the
hybrid device at an applied voltage of 2 V was much
lower than that of pure pearl-like GaP NWs (5.7 nA)
at the same condition, which could be attributed to
difficult charge transportation through the interface
of the PCBM and the pearl-like NWs without light
illumination. The result is in agreement with a
previously reported hybrid photodetector [7,10].
These results demonstrate that the PCBM and GaP
pearl-like NW hybrid film have enormously potential
applications as highly photosensitive detectors and
efficient photoswitches.
The above results demonstrate that the hybrid
device on rigid SiO2/Si substrate has an excellent
stability, reproducibility, and a fast detection time.
More importantly, it shows much improved
photocurrent and enhanced photoresponse
properties. This fact can be rationalized as following.
It is known that, due to high surface-to-volume ratio
of NWs, particularly for the pearl-like nanostructure,
trapping at the surface states drastically influence the
transport and photoconduction properties. For a
p-type NWs film based device, upon illumination
with a photo energy above the band-gap of GaP
(Eg~2.26 eV), electron-hole pairs are photogenerated
and electrons can be readily trapped at the NW
surface, leaving unpaired holes behind, which results
in an increase of the hole concentration, and then
leads to the increase of the conductivity of the GaP
NW [4]. Specially for the PCBM:GaP hybrid device,
the interface of the hybrid device plays a key role in
charge dissociation and transportation. It is generally
known that exciton dissociation can occur efficiently
at the two semiconductors mixed together in a
blended film, e.g. the system of an inorganic
semiconductor and an organic conjugated polymer in
a hybrid film [24-26]. The photoexcited electrons can
be readily transferred to the material with the higher
electron affinity, while the hole can be accepted by
the material with the lower ionization potential. Due
to the fact that GaP has a relatively low electron
affinity of 1.89 eV [27], while PCBM has a LUMO
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6 Nano Res.
level at around 4.3 eV [28], the possible band
alignment can be schematically plotted as the inset of
Figure S5. In this system, the photoexcited electrons
can be readily transferred to PCBM, leaving holes in
the GaP NW for photoconduction. This unique
configuration further improves the efficiency of
spatial separation of electron hole pairs leading to
higher photocurrent and prolonged photocarrier life
time.
Figure 3. Photoresponse properties of the flexible hybrid devices on PET substrate. (a) Schematic illustration of the hybrid
photodetector. The insets are the digital image and SEM image of the hybrid device. (b) Current versus voltage plots of the
hybrid device measured at room temperature in dark and under illumination with 550 nm light of different intensities. (c)
Photocurrent versus light intensity plot at a bias of 2 V. The corresponding function is I~P0.7. (d) Photocurrent versus time
plot of the device under illumination with 550 nm light at a bias of 2 V. (e) Zoom-in view of middle cycle at a bias of 2 V.
The light intensity is kept constant at 3.15 mW/cm2.
On the other hand, as the photoconductivity of
pure PCBM may affect the device performance,
photoresponse characteristics of the device made
from pure PCBM is also studied and shown in Figure
S6 in the supporting information. Notably, the dark
current (about 0.8 nA) in the pure PCBM device at an
applied voltage of 2V is much lower than that of pure
GaP NWs film (about 5.7 nA) and hybrid device
(about 2.2 nA) at the same condition. The result is in
agreement with previously hybrid device based on a
P3HT:PCBM blend [26]. Meanwhile, for the pristine
PCBM device, the photocurrent of 550 nm light
illumination was relatively low and about 4.3 nA,
which is much lower than the photocurrent of pure
GaP NWs film device (227.6 nA , shown in Figure 4d)
and the hybrid device (373.8 nA , shown in Figure
4d). This can be explained by much lower carrier
mobility in PCBM (0.21 cm2/Vs) as compared with
that in GaP NWs. In addition, in our hybrid system,
the GaP NWs are highly dispersed in the PCBM
matrix, forming a 3D interconnected network. The
unique structure results in a large interface area for
charge separation. Therefore, long-lived charge
separation and high transportation might be
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7 Nano Res.
achieved in the hybrid device. These results imply
that the performance enhancement of the hybrid
device is primarily contributed by the formation of
the junction interface and the favorable alignment of
the conduction band to prolong the carrier life time.
To explore the reason for the enhanced
photoresponse property, the UV-vis absorption
spectrum of a pure GaP NWs film, PCBM film and
PCBM:GaP NWs hubrid film (≈weight ratio of 3:5)
were measured and shown in Figure S7 in the
supporting information. From the spectrum, it can be
observed that the pure PCBM film depicts a main
absorption in the UV region with the peak at around
330 nm, and the pure pearl-like GaP film shows a
stronger absorption at the wavelength of 370 nm.
When pearl-like GaP NWs are mixed with PCBM, the
PCBM: GaP NWs hybrid film has the advantages of
both PCBM and GaP NWs and significantly broadens
the absorption spectra in the range of 320-450 nm,
which will be beneficial to efficient photo absorption
and exciton generation. These results indicate that
synergy effect made a tremendous contribution to
the enhanced photoresponse of the hybrid film.
After getting information about the electric
transport properties of the GaP NWs and the
photoresponse behavior of the hybrid PCBM:GaP
film, flexible photodetectors were then fabricated on
flexible PET substrate, as demonstrated in Figure 3a.
The as-fabricated flexible device can be operated
under bending state, revealing its excellent flexibility
which can be potentially used in flexible electronics.
The structures of the hybrid film was investigated by
SEM and the corresponding image is shown in
Figure 3a. It can be clearly observed that the
pearl-like GaP NWs were wrapped by the PCBM film,
indicating the good contact between the organic and
inorganic materials, which will benefit the charge
transportation through the interface between PCBM
and GaP NWs, and then improve the photoresponse
of the flexible hybrid device.
Figure 3b shows the I-V curves of the flexible
device when illuminated by light with wavelength of
550 nm and in dark, respectively. Obviously, the
photocurrent increases with the increased light
intensity ranged from 0.32 mW/cm2 to 3.15 mW/cm2,
which consists well with the rigid device on Si
substrate. By fitting the corresponding light-intensity
dependence of the photocurrent plotted in Figure 3c,
the power law function of I~P0.70 is obtained. Figure
3d presents the time-dependent photoresponse of the
flexible device measured by periodically turning the
light with a power density of 3.15 mW/cm2 on and off.
From the curves, we can find that the flexible device
shows superior sensitivity and stability to visible
illumination with the current on/off ratio of 60 at a
bias of 2.0 V. In addition, it is found (Figure 3d) that
the flexible device exhibited a dark current of 0.24 nA
and a photocurrent of 14.4 nA. Compared with the
hybrid device on rigid substrate (shown in Figure 2),
it is obviously seen that the photocurrent is much
smaller, which may attributed to the worse contact
between the pearl-like NWs and flexible PET
substrate, which fits well with the previous reports
on flexible devices [10,11]. Figure 3e shows a
individual photoresponse cycle obtained from the
time-dependent measurement in Figure 3d. The rise
time and decay time are found to be about 0.3s and
0.34s, respectively, which is comparable to that of the
device on rigid substrate.
Figure 4. I-T curves of the flexible hybrid devices on PET
substrate bent with various curvatures under a bias voltage
of 2V. The upper insets are the corresponding digital
photographs of the device under five bending states. The
lower inset show the I-V curves of the flexible hybrid
device on PET substrate without bending and after 20, 40,
60, 80, 100 and 120 cycles of bending, respectively.
In order to accommodate practical application of
the flexible photonic devices, not only the excellent
photoresponse characteristic but also the stability
and reliability is essentially needed. To get the
corresponding information, the flexible device was
fixed on two X-Y mechanical stages with a moving
step of 1 μm. Each end of the device was placed on
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8 Nano Res.
one stage. By adjusting the distance of the adjacent
stages, the bending curvature of the hybrid device
was precisely controlled. The electrical stability of the
flexible device based on PCBM:GaP hybrid film was
tested at various bending curvatures, accordingly. As
shown in Figure 4, five different bending stats of the
flexible device were recorded and labelled as state I,
II, III, IV, and V, respectively. As observed, the current
flow through the flexible device nearly kept
unchanged at five different states (the upper insets in
Figure 4), revealing that the conductance of the
hybrid film is hardly influenced by external bending
stress. In addition, the I-V curves of the flexible
device before and after bending for several cycles are
shown in lower insets of Figure 4. Bending of the
flexible device from states I to V followed by
releasing it back to state I was considered as one
cycle. From the curves, it can be seen that, compared
with the conductance of the device without bending
(the lower left inset in Figure 4), the conductance
endurance of the hybrid device (the lower right inset
in Figure 4) almost remains constant even after 20, 40,
60, 80, 100 and 120 cycles of bending, revealing the
good folding endurance of the flexible device. These
results demonstrate excellent electrical stability and
mechanical flexibility of the flexible PCBM:GaP
hybrid device.
Figure 5. Photoresponse properties of the flexible hybrid devices on (a-d) common sellotape and (e-f) PDMS substrate. (a)
Current versus voltage plots of flexible photodetector on sellotape substrate at different intensities. The upper left inset: the
digital image of the device. (b) Photocurrent versus light intensity plot at a bias of 2 V of the device on sellotape substrate.
The corresponding function are I~P0.72. (c) Photocurrent versus time plots of the device under illumination with light of
various wavelengths. (d) Zoom-in view of middle cycle at a bias of 2 V when illumination with a 550 nm light. (e) I-V plots
of flexible device on PDMS substrate in dark and under 550 nm light illumination. The upper left inset: Schematic
illustration of the device. (f) I-T plots of the flexible device on PDMS substrate at a bias of 2 V. The light intensity is kept
constant at 3.15 mW/cm2.
Highly flexible photodetectors were also fabricated on other flexible substrates to demonstrate the
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9 Nano Res.
feasibility of the current hybrid PCBM:GaP films.
Inset in Figure 5a shows the digital image of a
flexible device on sellotape, which was rolled into a
cylinder, indicating the excellent flexibility of the
device. Figure 5a exhibits a typical I-V curves of the
device measured under dark and a 550nm light
illumination at different intensities, respectively. It is
clearly shown that, at identical voltages, the
photocurrent of the device increases as the intensity
increases, which is in good agreement with the result
on either Si/SiO2 substrate (Figure 2) or PET substrate
(Figure 3). The corresponding light-intensity
dependence of the photocurrent can be fitted with
the power law, I~P0.72, also revealing excellent
photocapture in the hybrid film. Furthermore, the
reproducible on/off switching of the flexible device
on common sellotape (Figure 5c-d) further
demonstrates the superiority of the organic-inorganic
hybrid photodetector with a fast rise time (0.58 s) and
decay time (0.81 s). Flexible device was also
fabricated on polydimethylsiloxane (PDMS)
substrate and the corresponding results were
depicted in Figure 5e-f. The device also exhibits good
stability and reproducibility, and is sensitive to green
light (550 nm). All the above results indicate that all
the flexible device based on the PCBM:GaP NWs
hybrid film on different flexible substrates have
excellent stability, reproducibility, and a fast
detection time, which will exhibit good advantage for
application in the next generation high-sensitivity
and high-speed large scale organic-inorganic
photodetectors and photoswitches.
4 Conclusions
In conclusion, pearl-like GaP NWs were
synthesized via a simple CVD method, which were
mixed with PDMS to act as active materials for
highly flexible hybrid photodetectors on various
flexible substrate. Compared with the devices made
of either pure GaP NWs or PCBM, the hybrid device
exhibited an enhanced photoresponse characteristic
such as a fast response, increased photocurrent and
high photoresponse ration Besides, all the fabricated
flexible devices showed excellent flexibility, good
folding strength and high electrical stability and high
sensitivity to visible light. Our results demonstrate
that the organic-inorganic hybrid photodetectros
have promising potential for future application in
next generation of optoelectronic devices.
Acknowledgements
This work was supported by the National Natural
Science Foundation (91123008, 61377033), the 973
Program of China (No.2011CBA00703).
Electronic Supplementary Material: Supplementary
material (XRD pattern, EDX spectra, schematic
diagrams of the growth process of GaP nanowires;
photoresponse behavior and band gap diagrams of
the PCBM:GaP hybrid photodetectors;
photoresponse behavior of pure PCBM.) is available
in the online version of this article at
http://dx.doi.org/10.1007/s12274-***-****-*
(automatically inserted by the publisher). References
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Nano Res.
Electronic Supplementary Material
Flexible organic-inorganic hybrid photodetectors with
n-type PCBM and p-type pearl-like GaP nanowires
Gui Chen,† Xuming Xie,† and Guozhen Shen ()
Supporting information to DOI 10.1007/s12274-****-****-* (automatically inserted by the publisher)
FIGURE S1. XRD pattern of the as-grown pearl-like GaP nanowires.
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Nano Res.
FIGURE S2. EDS spectrum of the e, f part shown in Figure 1d.
FIGURE S3. Schematic diagrams of the growth process of the pearl-like GaP nanowires.
www.theNanoResearch.com∣www.Springer.com/journal/12274 | Nano Research
Nano Res.
FIGURE S4. (a). Photocurrent versus light intensity plot at a bias of 2 V. The corresponding function is I~P0.77.
(b). Single light on/off cycle transient response of the hybrid device at a bias of 2 V with light intensity of 3.15
mW/cm2.
FIGURE S5. Band diagrams of the PCBM:GaP hybrid film based photodetector.
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Nano Res.
FIGURE S6. Photoresponse characteristics of a device made from a pure PCBM film. (a). I-V curves of the
device in dark and under 550 nm green light illumination. (b). I-T curves of device under 550 nm illumination
measured for light-on and light off conditions at a 2 V applied voltage. The light intensity is kept constant at
3.15 mW/cm2.
FIGURE S7. UV-vis absorption spectra of a pure GaP NWs film (black), PCBM film (blue) and PCBM:GaP NWs
hybrid film (red) (≈weight ratio of 3:5).