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Highly efficient flexible piezoelectric nanogenerator and femtosecond two-photonabsorption properties of nonlinear lithium niobate nanowiresManoj Kumar Gupta, Janardhanakurup Aneesh, Rajesh Yadav, K. V. Adarsh, and Sang-Woo Kim
Citation: Journal of Applied Physics 121, 175103 (2017); doi: 10.1063/1.4982668View online: http://dx.doi.org/10.1063/1.4982668View Table of Contents: http://aip.scitation.org/toc/jap/121/17Published by the American Institute of Physics
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Highly efficient flexible piezoelectric nanogenerator and femtosecondtwo-photon absorption properties of nonlinear lithium niobate nanowires
Manoj Kumar Gupta,1,a) Janardhanakurup Aneesh,1 Rajesh Yadav,1 K. V. Adarsh,1
and Sang-Woo Kim2
1Department of Physics, Indian Institute of Science Education and Research, Bhopal, Bhopal Bypass Road,Bhauri, Bhopal, Madhya Pradesh 462066, India2School of Advanced Materials Science and Engineering, SKKU Advanced Institute of Nanotechnology(SAINT), Center for Human Interface Nanotechnology (HINT), and IBS Center for Integrated NanostructurePhysics, Institute for Basic Science (IBS), Sungkyunkwan University (SKKU), Suwon 440-746, South Korea
(Received 7 March 2017; accepted 15 April 2017; published online 3 May 2017)
We present a high performance flexible piezoelectric nanogenerator (NG) device based on the
hydrothermally grown lead-free piezoelectric lithium niobate (LiNbO3) nanowires (NWs) for scav-
enging mechanical energies. The non-linear optical coefficient and optical limiting properties of
LiNbO3 were analyzed using femtosecond laser pulse assisted two photon absorption techniques for
the first time. Further, a flexible hybrid type NG using a composite structure of the polydimethylsi-
loxane polymer and LiNbO3 NWs was fabricated, and their piezoelectric output signals were mea-
sured. A large output voltage of �4.0 V and a recordable large current density of about 1.5 lA cm�2
were obtained under the cyclic compressive force of 1 kgf. A subsequent UV-Vis analysis of the as-
prepared sample provides a remarkable increase in the optical band gap (UV absorption cut-off,
�251 nm) due to the nanoscale size effect. The high piezoelectric output voltage and current are dis-
cussed in terms of large band gap, significant nonlinear optical response, and electric dipole align-
ments under poling effects. Such high performance and unique optical properties of LiNbO3 show
its great potential towards various next generation smart electronic applications and self-powered
optoelectronic devices. Published by AIP Publishing. [http://dx.doi.org/10.1063/1.4982668]
INTRODUCTION
Lithium niobate (LiNbO3) is one of the most important
materials, which attracted massive attention because of its
fascinating physical properties such as piezoelectricity, ferro-
electricity, and nonlinear optical properties.1–3 LiNbO3 exhib-
its potential for novel applications by coupling the excellent
photostability, large piezoelectric charge coefficient, electro-
optic, nonlinear optical coefficients, and a large indirect band
gap of around 3.37 eV.4–7 Due to excellent electro-optic coef-
ficients, high thermal, mechanical, and chemical stabilities
and wide intrinsic bandwidth, LiNbO3 has wide scientific and
technological applications such as ultrafast modulation, fre-
quency conversion, tunable filter, and electro-optic modula-
tion.3,8–12 Further, several properties of LiNbO3 have been
extensively studied in the bulk form, but due to difficulties in
synthesizing at nanometer scales, its behaviour at nano-
dimensions is not well understood.13
Moreover, LiNbO3 is a well-known lead-free ABO3-type
perovskite that exhibits room-temperature ferroelectricity
with a larger spontaneous polarization of about 70 lC cm�2
and high ferroelectric transition temperature (�1483 K).5,14,15
The room temperature piezoelectricity and ferroelectricity of
LiNbO3 make it as a potential candidate for a new innovative
application as a flexible piezoelectric nanogenerator (NG) for
harvesting mechanical energy from the living environment
and the human body. For example, the mechanical energy
generated in the form of regular or irregular vibrations, such
as flow of body fluid, heartbeat, contraction of blood vessels,
muscle stretching eye blinking, walking, sound waves, air
flow, and so on, can be easily harvested by NGs.16–21 Various
NGs that convert mechanical energy into electrical energy
via the piezoelectric effect have been developed based on the
piezoelectric one-dimensional nanostructures of ZnO, InN,
GaN, KNbO3, and lead zirconate titanate (PZT) nanorods/
nanowires (NWs)/thin films and piezoelectric polymers.22–28
However, under mechanical pressure, the physical damage
of the device and breaking of NWs are most common
issues.28,29 Therefore, realization of high performance and
sustainable piezoelectric power output without damaging the
device is a challenging task for operating small electronic
devices such as light emitting diodes (LEDs), liquid crystal
displays (LCDs), and various self-powered nanosystems.
Moreover, it has been reported that as the size of the
particle reduces to the nanoscale, a drastic variation may
occur in their optical and electrical properties.30–33
Therefore, it is urgently required to understand the light
matter interactions in NWs of LiNbO3 and to measure its
non-linear optical coefficient for optoelectronic applications.
Among various techniques, the z-scan method is a popular,
simple, and effective tool for determining nonlinear proper-
ties, which provides the magnitudes of the real and imaginary
parts of the nonlinear susceptibility along with the sign of the
real part.34–36 Further, it has been shown that the pulse dura-
tion typically in the nano and pico-second time scales
strongly influences the nonlinearity.37,38 Therefore, determin-
ing nonlinearity in the femto-second time regime is a subject
a)Author to whom correspondence should be addressed. Electronic mail:
0021-8979/2017/121(17)/175103/7/$30.00 Published by AIP Publishing.121, 175103-1
JOURNAL OF APPLIED PHYSICS 121, 175103 (2017)
of great interest in order to design electro-optic and photonic
devices.39–42
In this work, we report the synthesis of LiNbO3 NWs
using the low-cost hydrothermal route for high efficient
mechanical to electric energy conversion and optoelectronic
applications. Structural and morphological characterizations
of LiNbO3 are also carried by X-ray diffraction (XRD), scan-
ning electron, and high-resolution transmission electron
microscopes (HR-TEM). Nonlinear optical properties were
investigated by the z-scan method using femtosecond laser
pulses. By utilizing the polydimethylsiloxane (PDMS) poly-
mer and LiNbO3 NWs, a composite-type flexible NG device
is developed. Through a periodic impact on the composite
NG by a linear motor, a piezoelectric output voltage and cur-
rent were obtained.
EXPERIMENTAL
Synthesis and fabrication of a LiNbO3 basednanogenerator
To synthesize the LiNbO3 NWs, high purity Nb2O5
and LiOH were mixed in the ratio of 1:10 in the distilled
water and subsequently stirred for 2 h. The mixture is
poured in a 50 ml Teflon lined stainless steel autoclave and
heated at 180 �C for 3 days in the oven. The white precipi-
tate was obtained after the mixture was cooled down to
room temperature. The final white product was washed
with distilled water and ethanol several times and dried at
120 �C for 12 h.
To fabricate flexible piezoelectric NGs, the powder of
LiNbO3 NWs was homogeneously mixed with the PDMS
polymer, and the resultant composite was spin-coated on an
indium tin oxide (ITO)-coated polyethylene terephthalate
(PET) substrate at 500 rpm for 15 s. A thin layer of the Cr/Al
film deposited on a plastic substrate serving as the electrode
of the piezoelectric NG was mechanically integrated on top
of the composite film. The effective area and thickness of the
device were 2 cm� 3 cm and 600 lm, respectively.
Characterization and measurements
The crystal structure of as-grown samples were investi-
gated by X-ray diffraction (XRD) with a Bruker D8 Advance
Cu-Ka1, k¼ 1.5401 A. Field-emission scanning electron
microscopy (FE-SEM) measurements were performed for
the morphological investigation. TEM images were obtained
using a JEOL JEM-2100F microscope. The UV-Vis optical
absorption spectrum was recorded using the Agilent Cary
5000 UV-VIS-NIR spectrophotometer. The third-order non-
linear optical properties of the LiNbO3 NWs were deter-
mined by the z-scan method using a femtosecond laser
system. A pushing tester (Labworks Inc., model no. pa-151
and ET-126B-4) was used to apply mechanical force to the
device. The output electric signal of the NG was recorded by
using a Tektronix DPO 3052 Digital phosphor oscilloscope
and a low-noise current preamplifier (model no. SR570,
Stanford Research Systems).
RESULTS AND DISCUSSION
The phase identification and the confirmation of crystal-
linity of the as-grown LiNbO3 NWs were investigated by the
powder XRD technique. The obtained XRD pattern of
LiNbO3 NWs at room temperature is shown in Fig. S1 (sup-
plementary material). The pattern shows that the diffraction
peaks are in agreement with JC-PDS #85-2456 and the for-
mation of the rhombohedral crystal system of the space
group R3c (166) with lattice constants a¼ b¼ 5.148 A and
c¼ 13.858 A.43 In addition to the LiNbO3 phase, small peaks
corresponding to the secondary phase of lithium niobate
(LiNb3O8) are also detected.
A typical FE-SEM image of the LiNbO3 NWs is shown
in Fig. 1(a), which reveals a well-defined NW morphology
with a diameter in the range of 250–500 nm and a length of
about 10–15 lm. HR-TEM was employed to study the size
and crystalline quality of the LiNbO3 NW (Figs. 1(b)–1(d)).
The HR-TEM image exhibits clear fringes with spaces of 0.
375 nm and 0.170 nm, which are in good agreement with the
interplanar spacing of (012) and (116) planes (Fig. 1(c)). The
crystalline nature of the LiNbO3 NW can be confirmed by its
corresponding fast Fourier transform (FFT) pattern. The dif-
fraction spots can be indexed to the rhombic phase of
LiNbO3 where regular and bright spots of the selected area
electron diffraction (SAED) indicate the crystalline feature
(Fig. 1(d)).
Figure 2 depicts a UV–Vis optical absorption spectrum
of the as-prepared LiNbO3 NWs, which shows a strong
absorption band-edge around 250 nm that is significantly
smaller than the bulk LiNbO3 single crystal (315 nm) by Guo
et al.44 Interestingly, the observed band gap of lithium nio-
bate in the present study is well correlated with a theoretically
calculated band gap value (�4.71 eV) for the ferroelectric
phase of LiNbO3.45 The obtained cut-off indicates that as-
grown LiNbO3 NWs have comparatively larger band gap
than previous reports, which facilitates its versatile applica-
tions in optoelectronic devices.44–47 The high value of the
band gap is attributed to the size-quantization effect induced
discrete energy spectrum in the conduction band and forma-
tion of energy levels in the forbidden gap appeared due to
surface defects.45 It is also expected that the exciton energy
spectrum modified by spatial confinement of the exciton
wave functions can result in an increase in the band gap of
LiNbO3.45,47 Further, it is well known that piezopotential
generation is significantly affected by free charge carriers of
LiNbO3 NWs. Therefore, the optical band gap of LiNbO3
also plays an important role in defining piezoelectric output
voltage/current because of the piezoelectric potential screen-
ing effect induced by the presence of the free carrier density.
Therefore, a comparatively large band gap of as grown
LiNbO3 NWs may lead to a high output piezoelectric signal
under the mechanical pressure.
An open aperture z-scan technique was used for the mea-
surement of the nonlinear absorption (NLA) coefficient of
LiNbO3 NWs.48 The experiments were carried out at 560 nm
using 120 fs pulses generated by using an optical parametric
amplifier. The details of the experimental procedures are
described in the supplementary material. The obtained spectra
175103-2 Gupta et al. J. Appl. Phys. 121, 175103 (2017)
from open aperture z-scan measurement at two different
wavelengths are shown in Fig. 3(a). The measurements were
carried out with an on-axis peak intensity of 78 GW cm�2. It
can be seen that for 800 nm photon light, LiNbO3 NWs do not
show any significant non-linear absorption, whereas for
560 nm, it exhibits non-linear absorption. Further, a decrease
in transmittance as a function of input intensity is also
observed, which clearly indicates the presence of non-linear
absorption in the LiNbO3 NWs for 560 nm photons (Fig.
3(b)). This behavior of NLA in LiNbO3 NWs under two dif-
ferent excitation wavelengths can be easily understood in
terms of the band gap of LiNbO3 as shown in the schematic
diagram of Fig. S2. It is obvious that in the case of the 800 nm
laser beam, the photon energy (1.55 eV) is below the band
gap of LiNbO3. Therefore, transition of electrons from the
valence band to the conduction band is not possible for
800 nm photons, which results in no nonlinear absorption.
Interestingly, although the photon energy of 560 nm (2.21 eV)
is still less than the band gap of LiNbO3, the two photon
energy was sufficient to induce electron transitions from
the valence band to the conduction band in LiNbO3 NWs
as confirmed in the obtained result. Moreover, at the lower
intensity side, there is no significant absorption for 560 nm.
Nevertheless, at the higher intensity side, a significant reduc-
tion in transmittance is measured, which is due to the increase
in the density of photons that increases the probability of
simultaneous absorption of two photons (usually known as a
two photon absorption (TPA) process).
In the case of two photon absorption (TPA), the normal-
ized light transmittance for a laser pulse having both tempo-
ral and spatial Gaussian profiles is given by48
T ¼ 1
Q zð Þffiffiffippð1�1
ln 1þ Q zð Þx2� �
dx; (1)
where
Q zð Þ ¼bI0Lef f
1þ z
zr
� �2:
b is the two photon absorption coefficient, I0 is the peak
intensity at focus in the absence of the sample, Zr is the
Rayleigh length for the focusing lens, z is the sample posi-
tion with respect to the focus (z¼ 0), and Lef f ¼ 1�e�aLð Þa is
the effective length for a sample having thickness L, where ais the linear absorption coefficient.
The nonlinear absorption coefficient b was obtained by
curve fitting of Equation (1) for the experimental z-scan dataFIG. 2. UV-Vis spectrum of the LiNbO3 NWs.
FIG. 1. Scanning electron microscopy
(SEM) image (a) of the LiNbO3 NWs
with an average diameter of 300 nm
and a length in the range of 10–15 lm.
(b) Transmission electron microscopy
image. (c) The lattice fringe image
for (012) and (116) with its (d) FFT
transformation.
175103-3 Gupta et al. J. Appl. Phys. 121, 175103 (2017)
of the excitation wavelength at 560 nm. The two photon
absorption coefficient b is found to be 0.13 6 0.02 mm
GW�1. This value is slightly smaller as compared to the pre-
viously reported bulk form of LiNbO3.49 The decrease in the
b is due to the nanocrystalline size of LiNbO3, which is con-
sistent with the recent studies.50 However, in order to estab-
lish the relationship of the optical nonlinearity with crystallite
size, extensive work on varying sizes is required. The optical
limiting property of the LiNbO3 NWs was also investigated.
Fig. 3(c) shows the output intensity through the sample as a
function of input intensity. It can be seen that at the lower
intensity side, the output intensity is linearly proportional to
the input intensity; however, as the input intensity increases
up to a certain value, it starts deviating from its linear behav-
ior. The results indicate that LiNbO3 NWs are well suitable
for optical limiting applications such as protection of human
eyes and sensors from intense laser radiations, in which
blocking or limiting the high-intensity beams is required.
Further, owing to its well-known piezoelectric property
of LiNbO3, we demonstrated alternative-current (AC) power
generation from piezoelectric NGs as a potential application
of these LiNbO3 NWs. A robust flexible NG device was
designed to harvest mechanical energy from the living
environment. A composite type flexible NG was fabricated
using a device structure of the ITO coated PET substrate/
(LiNbO3:PDMS) with an aluminum (Al) top electrode as
shown in Fig. 4. An ITO coated PET substrate was used as
the bottom electrode and as a flexible substrate. The sche-
matic diagram of device fabrication is shown in Fig. S3.
Initially, a mixture of the LiNbO3 NW and PDMS polymer
with a volume ratio of 40:60 was prepared and then spin
coated on the ITO/PET substrate at 1000 rpm for 15 s. In
order to prepare the top electrode, a thin layer of Al was
deposited on the Cr coated flexible polyethylene-naphthalate
(PEN) substrate and then carefully mechanically integrated
with the top of the composite layer to form a complete NG
device. A schematic diagram and original photo image of the
practical device are shown in Figs. 4(a) and 4(b), respec-
tively. The FE-SEM analysis of the LiNbO3:PDMS sample
was carried out, to gain insights into the NW distribution
behavior, as shown in Figs. 4(c) and 4(d). The low and high
magnified SEM images confirmed that LiNbO3 NWs are
FIG. 3. Open aperture z-scan curve for LiNbO3 NWs dispersed in ethanol: (a) the variation of normalized transmitted intensity as a function of position, (b)
input intensity (solid line represents the theoretical fit), and (c) optical limiting curve showing the deviation from linear behaviour for higher input intensity.
FIG. 4. (a) Schematic diagrams of the
flexible PDMS assisted LiNbO3NW
based piezoelectric NG, (b) original
photo image of the flexible NG on the
transparent ITO/PET substrate and the
top view of the composite (inset), and
(c) low and (d) high magnified-SEM
images of the LiNbO3: PDMS composite.
175103-4 Gupta et al. J. Appl. Phys. 121, 175103 (2017)
randomly distributed inside the PDMS polymer. From the
cross-sectional FE-SEM images shown in Fig. S4, the thick-
ness of the composite layer was estimated to be about 350 lm.
Fourier transform infrared spectroscopy (FT-IR) spectra were
also measured in order to obtain physical insights into the
chemical bonding and phase formation in the PDMS:LiNbO3
composite (Fig. S5). The result of FT-IR is discussed in the
supplementary material.
The piezoelectric output voltage and current generated
from a composite LiNbO3:PDMS based hybrid NG were
obtained under periodic vertical pushing and releasing condi-
tions using the computer interface force simulator. An output
voltage of about 4.0 V and a current density of about 1.5 lA
cm�2 were obtained under a vertical compression of 1 kgf
at a frequency of 4 Hz (sinusoidal vibration) as shown in
Figs. 5(a)–5(d) and 6, respectively. The device was electri-
cally poled before the piezoelectric signal measurement with
a dc electric field of about 90 kV/cm at room temperature.
It is noteworthy that the electric dipoles can be easily ori-
ented or switched in a particular direction after applying a
suitable electric field due to the ferroelectric property of the
LiNbO3 NW.6,7
To confirm that the measured signal was from the
NG rather than the instruments, we performed “switching-
polarity” tests. As predicated, when the voltage meter/
current meter was forward connected to the NG (i.e., positive
and negative probes were connected to the positive and nega-
tive electrodes, respectively), positive pulses were recorded
during the pushing and when the voltage meter/current meter
was connected in reverse, the output pulses were also
reversed as shown for output voltage (Figs. 5(a) and 5(c))
and output current (Figs. 6(a) and 6(b)). Enlarged views of
one cycle of output voltage (Figures 5(b) and 5(d)) and out-
put current (Figs. S6 and S7 of supplementary material) were
given for further verification of the piezoelectric reversible
signal under pushing and releasing conditions. It is notewor-
thy that generated output voltage from the device was almost
10 times and output current was almost 150 times higher
than the previously reported LiNbO3 based NG (0.46 V,
9.11 nA).51 This drastic enhancement of output voltage and
FIG. 5. (a) Piezoelectric output voltage
generated from the LiNbO3 NW:PDMS
based NG under compressive force
(forward connection), (b) enlarged view
of one cycle of output voltage under
forward connection, (c) output voltage
under reverse connection (switching-
polarity test), and (d) enlarged view of
one cycle of output voltage under
reverse connection.
FIG. 6. (a) Piezoelectric output voltage
generated from the LiNbO3 NW:PDMS
based NG under compressive force (for-
ward connection) and (b) output current
under reverse connection (switching-
polarity test).
175103-5 Gupta et al. J. Appl. Phys. 121, 175103 (2017)
current may be due to the comparatively large band gap. It is
expected that due to the large band gap and therefore com-
paratively small free charge carriers in LiNbO3 NWs, the
piezoelectric screening effect reduces, which results in high
piezoelectric output performance. A comparison of output
performance of other reported composite type piezoelectric
NGs is given in the supplementary material (Table S1).
Further, it was also reported that the formation of the second-
ary phase such as LiNb3O8 (niobium-rich grain boundaries)
in the lithium niobate phase decreases the piezoelectric
charge coefficient, which indicates that the piezoelectric out-
put voltage/current can be further reduced.52 Interestingly, in
contrast to expectation, piezoelectric output voltage/current
from the as-grown LiNbO3 sample based NG (which con-
tains a small amount of the LiNb3O8 phase) was much higher
than the previously reported LiNbO3 based NG. Therefore,
we proposed that enhancement of piezoelectric output volt-
age and current from the NG device is mainly due to the dra-
matic increase in the band gap and reduction of screening of
piezoelectric polarisation charges by free carriers. It is worth
to point out that no significant output voltage was observed
from only the PDMS based NG under the same compressive
force.
The working principle of the piezoelectric NG device for
generating the electrical signal is presented in Fig. 7. In the
absence of any external pressure (and/or electric field), no
piezo-induced electric charge is generated due to zero net
dipole moment, and therefore, no electric signal is detected
(Fig. 7(a)). However, when an external pushing force is verti-
cally applied to the top electrode of the electric poled NG
device, the electric dipoles of LiNbO3 presented in the matrix
are strongly aligned due to the poling effect. Consequently, a
piezoelectric potential is created due to mechanical deforma-
tion of the device. As a result, overall polarization across the
electrodes changes and a significant piezoelectric potential
across the external electrodes is produced during pushing
(positive pulse). Further, when the vertical compressive force
is released, the piezoelectric effect is disappeared, and the
accumulated charges at the bottom electrode side move back
to the opposite direction and an electric signal in the reverse
direction is obtained (Fig. 7(b)).
CONCLUSIONS
In summary, we demonstrated the growth of large scale
synthesis of LiNbO3 NWs using the low-cost hydrothermal
solution technique. Nonlinear optical analysis and optical
limiting properties of LiNbO3 were investigated via the two
photon absorption technique using femtosecond laser pulses.
The flexible piezoelectric NG device was fabricated using
the composite of the PDMS polymer and lead-free LiNbO3
NWs. Under vertical periodic compressive force, a large out-
put voltage about 4.0 V and a very large current density of
about 1.5 lA cm�2 were obtained under the cyclic compres-
sive force. The output current was 150 times higher than the
previously reported LiNbO3 based NG. To align the electric
dipoles of ferroelectric/piezoelectric LiNbO3 inside the poly-
mer matrix, the electric poling method was employed. To
understand the enhancement of output performance, UV-ViS
and femtosecond laser studies were also carried out. We
have shown that large piezoelectric output voltage/current
from the composite NG is strongly affected by the large
band gap and nonlinear properties of LiNbO3. Such a result
can be exploited for harvesting mechanical energy and for
piezoelectronics and piezo-phototronic applications due to
their multifunctional properties.
SUPPLEMENTARY MATERIAL
See supplementary material for the XRD pattern of
LiNbO3 NWs, experimental details of two-photon absorp-
tion, the schematic image of two photon induced transition,
schematic diagrams of the piezoelectric nanogenerator
device fabrication process, the cross-sectional FE-SEM
image of the LiNbO3:PDMS composite, FT-IR spectra of the
LiNbO3:PDMS composite, the enlarged view of one cycle of
output current under forward and reverse connections under
mechanical stress, and a table showing the comparison of
output performance of the NG present here with other
reported composite type NGs.
ACKNOWLEDGMENTS
M.K.G. is grateful to the Department of Science &
Technology, Government of India, for awarding the DST-
INSPIRE Faculty Fellowship [IFA-13 PH-81].
1C. Braun, S. Sanna, and W. G. Schmidt, J. Phys. Chem. C 119, 9342
(2015).2A. V. Ievlev, S. Jesse, A. N. Morozovska, E. Strelcov, E. A. Eliseev, Y. V.
Pershin, A. Kumar, V. Ya. Shur, and S. V. Kalinin, Nat. Phys. 10, 59–66
(2014).3A. Guarino, G. Poberaj, D. Rezzonico, and R. Deglinnocenti, Nat.
Photonics 1, 407 (2007).4D. Xue and X. He, Phys. Rev. B 73, 64113 (2006).
FIG. 7. Schematic illustration of the power generation mechanism from a piezoelectric LiNbO3 based NG: (a) nanowires and their corresponding electric
dipoles are randomly oriented inside the PDMS matrix, and no piezoelectric charge is produced in the absence of mechanical force. (b) Piezoelectric charges
are generated in the electric poled device under the application of force and electrons started to flow from the top electrode to the bottom electrode, and the
positive electric signal is detected.
175103-6 Gupta et al. J. Appl. Phys. 121, 175103 (2017)
5X. Zhang and D. Xue, J. Phys. Chem. B 111, 2587–2590 (2007).6R. Grange, J. W. Choi, C. L. Hsieh, Y. Pu, A. Magrez, R. Smajda, L.
Forro, and D. Psaltis, Appl. Phys. Lett. 95, 143105 (2009).7M. L. Bortz, L. A. Eyres, and M. M. Fejer, Appl. Phys. Lett. 62, 2012
(1993).8T. Kawanishi, S. Oikawa, K. Higuma, M. Sasakl, and M. Izutsu, IEICE
Trans. Electron. E85-C, 150–155 (2002).9K. Suizu and K. Kawase, IEEE J. Sel. Top. Quantum Electron. 14,
295–306 (2008).10Y. Ishigame, T. Suhara, and H. Nishihara, Opt. Lett. 16, 375 (1991).11K. Thyagarajan, J. Lugani, S. Ghosh, K. Sinha, A. Martin, D. B.
Ostrowsky, O. Alibart, and S. Tanzilli, Phys. Rev. A 80, 052321 (2009).12K. Nakamura, Y. Kurosawa, and K. Ishikawa, Appl. Phys. Lett. 68, 2799
(1996).13X. Sun, Y. J. Su, X. Li, K. W. Gao, and L. J. Qiao, J. Appl. Phys. 111,
094110 (2012).14A. A. Belik, T. Furubayashi, H. Yusa, and E. Takayama Muromachi,
J. Am. Chem. Soc. 133, 9405 (2011).15D. D. Fong, G. B. Stephenson, S. K. Streiffer, J. A. Eastman, O. Auciello,
P. H. Fuoss, and C. Thompson, Science 304, 1650 (2004).16M. K. Gupta, S. W. Kim, and B. Kumar, ACS Appl. Mater. Interfaces 8,
1766 (2016).17G. C. Yoon, K.-S. Shin, M. K. Gupta, K. Y. Lee, J.-H. Lee, Z. L. Wang,
and S.-W. Kim, Nano Energy 12, 547 (2015).18K. Y. Lee, M. K. Gupta, and S.-W. Kim, Nano Energy 14, 139
(2015).19C.-Y. Sue and N. C. Tsai, Appl. Energy 93, 390 (2012).20Z. Li and Z. L. Wang, Adv. Mater. 23, 84 (2011).21Z. Li, G. Zhu, R. Yang, A. C. Wang, and Z. L. Wang, Adv. Mater. 22,
2534 (2010).22Z. L. Wang and J. H. Song, Science 312, 242 (2006).23M. K. Gupta, J. H. Lee, K. Y. Lee, and S.-W. Kim, ACS Nano 7, 8932
(2013).24C. T. Huang, J. H. Song, C. M. Tsai, W. F. Lee, D. H. Lien, Z. Y. Gao, Y.
Hao, L. J. Chen, and Z. L. Wang, Adv. Mater. 22, 4008 (2010).25C. Y. Chen, G. Zhu, Y. F. Hu, J. W. Yu, J. H. Song, K. Y. Cheng, L. H.
Peng, L. J. Chou, and Z. L. Wang, ACS Nano 6, 5687 (2012).26K. I. Park, J. H. Son, G. T. Hwang, C. K. Jeong, J. Ryu, M. Koo, I. Choi,
S. H. Lee, M. Byun, Z. L. Wang, and K. J. Lee, Adv. Mater. 26, 2514
(2014).27Y. C. Mao, P. Zhao, G. McConohy, H. Yang, Y. X. Tong, and X. D.
Wang, Adv. Energy Mater. 4, 1301624 (2014).28R. S. Weis and T. K. Gaylord, Appl. Phys. A: Mater. Sci. Process. 37, 191
(1985).
29M.-R. Joung, H. Xu, I.-T. Seo, D.-H. Kim, J. Hur, S. Nahm, C.-Y. Kang,
S.-J. Yoon, and H.-M. Park, J. Mater. Chem. A 2, 18547 (2014).30G. Zhu, R. Yang, S. Wang, and Z. L. Wang, Nano Lett. 10, 3151 (2010).31K. H. Kim, B. Kumar, K. Y. Lee, H. K. Park, J. H. Lee, H. Lee, H. Jun, D.
Lee, and S.-W. Kim, Sci. Rep. 3, 2017 (2013).32J. Junquera and P. Ghosez, Nature 422, 506 (2003).33F. R. Hu, H. C. Zhang, C. Sun, C. Y. Yin, B. H. Lv, C. F. Zhang, W. W.
Yu, X. Y. Wang, Y. Zhang, and M. Xiao, ACS Nano 9, 12410 (2015).34M. A. Fakhri, Y. A. Douri, U. Hashim, E. T. Salim, D. Prakash, and K. D.
Verma, Appl. Phys. B 121, 107 (2015).35K. Wang, J. Zhou, L.-Y. Yuan, Y.-T. Tao, J. Chen, P.-X. Lu, and Z.-L.
Wang, Nano Lett. 12, 833 (2012).36B. S. Kalanoor, L. Gouda, R. Gottesman, S. Tirosh, E. Haltzi, A. Zaban,
and Y. R. Tischler, ACS Photonics 3, 361 (2016).37H. Chen, B. Yang, M. Zhang, F. Wang, K. Cheah, and W. Cao, Mater.
Lett. 64, 589 (2010).38M. Kauranen and A. V. Zayats, Nat. Photonics 6, 737 (2012).39H. Li, Y. Jia, Q. Xu, K. Shi, J. Wu, P. C. Eklund, Y. Xu, and Z. Liu, Appl.
Phys. Lett. 96, 021103 (2010).40A. J. Schellekens, K. C. Kuiper, R. R. J. C. de Wit, and B. Koopmans, Nat.
Commun. 5, 4333 (2014).41D. Kim, H. Choi, S. Yazdanfar, and P. T. C. So, Microsc. Res. Tech. 71,
887–896 (2008).42H. Choi and P. T. C. So, Sci. Rep. 4, 6626 (2014).43A. C. Santulli, H. Zhou, S. Berweger, M. B. Raschke, E. Sutter, and S. S.
Wong, CrystEngComm. 12, 2675 (2010).44E.-J. Guo, J. Xing, K.-J. Jin, H.-B. Lu, J. Wen, and G.-Z. Yang, J. Appl.
Phys. 106, 023114 (2009).45C. Thierfelder, S. Sanna, A. Schindlmayr, and W. G. Schmidt, Phys.
Status Solidi C 7, 362 (2010).46W. G. Schmidt, M. Albrecht, S. Wippermann, S. Blankenburg, E. Rauls,
F. Fuchs, C. R€odl, J. Furthm€uller, and A. Hermann, Phys. Rev. B 77,
035106 (2008).47S. Kase and K. Ohi, Ferroelectrics 8, 419 (1974).48M. S. Bahae, D. Hutchings, D. J. Hagan, and E. W. V. Stryland, IEEE J.
Quantum Electron. 26, 760 (1990).49S. M. Kostritskii and M. Aillerie, J. Appl. Phys. 111, 103504 (2012).50L. A. Padilha, J. Fu, D. J. Hagan, E. W. V. Stryland, C. L. Cesar, L. C.
Barbosa, C. H. B. Cruz, D. Buso, and A. Martucci, Phys. Rev. B 75,
075325 (2007).51B. K. Yun, Y. K. Park, M. Lee, N. Lee, W. Jo, S. Lee, and J. H. Jung,
Nanoscale Res. Lett. 9, 4 (2014).52A. Z. Simoes, A. H. M. Gonzalez, A. A. Cavalheiro, M. A. Zaghete, B. D.
Stojanovic, and J. A. Varela, Ceram. Int. 28, 265 (2002).
175103-7 Gupta et al. J. Appl. Phys. 121, 175103 (2017)