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Effect of flexoelectricity on the electromechanical responseof graphene nanocomposite beam
S. I. Kundalwal . K. B. Shingare . Ankit Rathi
Received: 7 September 2018 / Accepted: 17 September 2018
� Springer Nature B.V. 2018
Abstract Owing to its unique multifunctional and
scale-dependent physical properties, graphene is
emerged as promising reinforcement to enhance the
overall response of nanotailored composite materials.
Most recently, the piezoelectricity phenomena in
graphene sheets was found through interplay between
different non-centrosymmetric pores, curvature and
flexoelectricity phenomena. This has added new
multifunctionality to existing graphene and it seems
the use of piezoelectric graphene in composites has yet
to be fully explored. In this article, the mechanics of
materials and finite element models were developed to
predict the effective piezoelectric and elastic (piezoe-
lastic) properties of the graphene reinforced nanocom-
posite material (GRNC). An analytical model based on
the linear piezoelectricity and Euler beam theories was
also developed to investigate the electromechanical
response of GRNC cantilever beam under both
electrical and mechanical loads accounting the flex-
oelectric effect. Furthermore, molecular dynamics
simulations were carried out to determine the elastic
properties of graphene which were used to develop the
analytical and numerical models herein. The current
results reveal that the flexoelectric effect on the elastic
behavior of bending of nanocomposite beams is
significant. The electromechanical behavior of GRNC
cantilever beam can be tailored to achieve the desired
response via a number of ways such as by varying the
volume fraction of graphene layer and the application
of electrical load. Our fundamental study highlights
the possibility of developing lightweight and high
performance piezoelectric graphene based nanoelec-
tromechanical systems such as sensors, actuators,
switches and smart electronics as compared with the
existing heavy, brittle and toxic piezoelectric
materials.
Keywords Graphene � Flexoelectricity �Piezoelectricity � Nanocomposite � Micromechanics �Finite element
1 Introduction
Flexoelectricity phenomenon is the response of elec-
tric polarization to an applied strain gradient and is
developed as a consequence of crystal symmetry in all
materials. Recent advances in nanoscale technologies
have renewed the interest in flexoelectricity due to the
obvious existence of large strain gradients at the
nanoscale level that leads to strong electromechanical
S. I. Kundalwal (&) � K. B. Shingare � A. RathiApplied and Theoretical Mechanics (ATOM) Laboratory,
Discipline of Mechanical Engineering, Indian Institute of
Technology Indore, Indore 453552, India
e-mail: [email protected]
K. B. Shingare
e-mail: [email protected]
A. Rathi
e-mail: [email protected]
123
Int J Mech Mater Des
https://doi.org/10.1007/s10999-018-9417-6(0123456789().,-volV)(0123456789().,-volV)
coupling. The symmetry breaking at surfaces and
interfaces in nonpolar materials allows new forms of
electromechanical coupling such as surface piezoelec-
tricity and flexoelectricity, which cannot be induced in
the bulk materials. Piezoelectricity–electrical polar-
ization induced by a uniform strain (or vice versa)—is
the most widely known and exploited forms of
electromechanical coupling that exists in non-cen-
trosymmetric crystals. In non-centrosymmetric crys-
tals, the absence of the center of inversion results in the
presence of bulk piezoelectric properties. In contrast to
piezoelectricity, flexoelectricity can be found in any
crystalline material, regardless of the atomic bonding
configuration (Kundalwal et al. 2017). Piezoelectric
materials are commonly used where precise and
repeatable controlled motion is required such as
atomic force microscopy probes, smart structures,
and sensors and actuators (Kundalwal et al. 2013). The
conventional piezoelectric materials in the form of
piezoceramics are brittle, bulky and also sensitive due
to the content of high lead which is hazardous to the
environment (Bernholc et al. 2004). On the other hand,
piezoelectric polymers are light weight and environ-
mentally friendly, but typically show weaker piezo-
electric response. As compared to the existing
piezoelectric materials, there is always search for
light weight, high performance and environmentally
benign new piezoelectric materials.
The successful synthesis of 2D single layer
graphene sheet byNovoselov et al. (2004) has attracted
considerable attention from both academia and indus-
try. This is due to its unique scale-dependent elec-
tronic, mechanical and thermal properties (Zhang et al.
2005; Balandin et al. 2008; Lee et al. 2008; Gupta and
Batra 2010; Shah and Batra 2014a; Verma et al. 2014;
Alian et al. 2017; Kundalwal et al. 2017). It is widely
considered to be one of the most attractive materials of
the twenty-first century. Most recently, the piezoelec-
tric effect in non-piezoelectric graphene layers is found
by Kundalwal et al. (2017) using flexoelectric phe-
nomenon via quantum mechanics calculations. This
study showed that the presence of strain gradient in
non-piezoelectric graphene sheet does not only affect
the ionic positions, but also the asymmetric redistri-
bution of the electron density, which induces strong
polarization in the graphene sheet. The resulting axial
and normal piezoelectric coefficients of the graphene
sheet were determined using two loading conditions:
(1) a graphene sheet containing non-centrosymmetric
pore subjected to an axial load and (2) a pristine
graphene sheet subjected to a bending moment. The
results further revealed that the respective axial and
normal electromechanical couplings in graphene can
be engineered by changing the size of non-centrosym-
metric pores and radii of curvature.
Unique 2D structure and properties, and as it is a
semiconductor with zero bandgap make graphene
particularly suitable for nanoelectromechanical sys-
tems (NEMS) applications. In recent advances, it is
widely used as an energy harvester and in the NEMS
applications. Beams and cantilevers are two important
types of NEMS structures, and the latter one has more
potential application due to its linear behavior and
high sensitivity. Graphene beams have been exten-
sively studied in the last decade (Li et al. 2012 and
references therein), however, to date, a very few
researchers studied graphene-based cantilever beam
due to its challenging structure and fabrication. For
instance, Conley et al. (2011) proposed practical
realization of the strain-engineering scheme to control
electron properties of graphene cantilevers subjected
to significant variation of strain. Free-standing carbon
nanomaterial hybrid sheets, consisting of carbon
nanotubes (CNTs), exfoliated graphite nanoplatelets
and nanographene platelets, have been prepared by
Hwang et al. (2013) using various material combina-
tions and compositions. When subjected to tensile
strains, these carbon nanomaterial sheets showed
piezoresistive behavior, characterized by a change in
electrical resistance with applied strain. Kvashnin
et al. (2015) reported that a graphene sheet does not
show any polarization until the instantaneous quantum
fluctuative is responsible for the van der Waals
interactions. Da Cunha Rodrigues et al. (2015) studied
the electromechanical properties of a single-layer
graphene transferred onto SiO2 calibration grating
substrates via piezoresponse force microscopy and
confocal Raman spectroscopy. The calculated vertical
piezocoefficient of graphene was found about
1.4 nm V-1, that is, much higher than that of
conventional piezoelectric materials such as lead
zirconate titanate and comparable to that of relaxor
single crystals. The observed piezoresponse and
achieved strain in graphene are associated with the
chemical interaction of graphene’s carbon atoms with
the oxygen from underlying SiO2. The results provide
a basis for future applications of graphene layers for
sensing, actuating and energy harvesting.
123
S. I. Kundalwal et al.
Recently, metal matrix composite fascinated the
attention of the researchers because of its high
mechanical properties and specific stiffness. To
achieve increasing demands of high energy efficiency
and mechanical strength of material, many researchers
experimentally introduced the CNT-reinforced alu-
minium composites (CNT/Al) over the last two
decades. It is very critical to mix or disperse CNTs
uniformly in the aluminium matrix without decaying
their properties. Therefore, the graphene in the form of
graphene nanosheets (GNs) and graphene nanoplate-
lets (GNPs) were incorporated into the aluminium
matrix in the literature. For example, graphene
reinforced aluminum matrix fabricated using different
methods such as spark plasma sintering, flake powder
metallurgy and semi-solid powder processing (Wang
et al. 2012; Bastwros and Kim 2016; Tian et al. 2016;
Chen et al. 2018). They have studied the various
synthesis methods and showed the excellent enhance-
ment of mechanical properties with mere 0.3 wt% over
the pure aluminium matrix. Saber et al. (2014)
developed hybrid PZT based piezoelectric composite
for sensory applications by incorporating the thin film
of multi-walled carbon nanotubes (MWCNTs) and
GNPs. The nanocomposite films showed significant
improvement in the effective piezoelectric and stiffnes
properties of resulting nancomposite by * 50% and
200%, respectively. They also reported that the use of
GNPs in composite is better than MWCNTs when the
dynamic response and poling behavior are considered.
Kandpal et al. (2017) elucidated the role of addition of
GNPs into the nanocomposite for the improvement of
piezopotential response such as output voltage of
nanogenerator which can be used as an energy
harvester. Graphene oxide (GO), a derivative of
graphene, is also found the application in NEMS
because of its chemical reduction shows promising
route towards the bulk production of graphene for
commercial applications (Cui et al. 2016). Bhavanasi
et al. (2016) introduced the bilayer film made of
PVDF-TrFE and GO which exhibited extraordinary
energy harvesting performance with efficient transfer
of electromechanical energy. In their extensive
research, they concluded that GO film enhanced
voltage output and power density approximately by
2 times and 2.5 times, respectively, over that of PVDF-
TrFE film. Dasari et al. (2018) experimentally inves-
tigated GO-reinforced aluminum composite using the
liquid phase mixing and powder metallurgy
techniques.
A few analytical studies have also been conducted
to incorporate the effect of flexoelectricity which
identified some of its unexpected manifestations in
structural elements. Gharbi et al. (2011) observed an
important role of flexoelectricity in the hardening of
ferroelectrics at nano-indentation. Morozovska et al.
(2011) reported that the flexoelectricity plays an
important role in the electromechanical responce of
moderate conductors. The influence of the flexoelec-
tric effect on the mechanical and electrical properties
of bending piezoelectric nanobeams with different
boundary conditions was investigated by Yan and
Jiang (2013). A size-dependent model of a three-layer
microbeam including a flexoelectric dielectric layer
was proposed by Li et al. (2014) based on the theory
presented by Hadjesfandiari (2013). Rupa and Ray
(2017) obtained the exact solutions for the static
response of simply supported flexoelectric nanobeam.
The beam was subjected to the applied mechanical
load on its top surface while it was activated with the
prescribed voltage at its top and bottom surfaces.
The ability to fabricate NEMS with engineered
properties, based on stacking of weakly van der Waals
(vdW) interacting atomically thin layers, is quickly
becoming reality, and this has stimulated a new
research on graphene based composites. To the best of
current authors’ knowledge, a flexible piezoelectric
graphene-based cantilever beam that offers various
possibilities for developing NEMS has not been
studied yet which may represent an alternative to the
conventional piezoelectric nanostructures. This is
indeed the motivation behind the current study. As a
strikingly novel research goal, we focus on the
development of (1) analytical and numerical microme-
chanics models to determine the piezoelastic proper-
ties of GRNC, (2) a theoretical piezoelasticity model
for the GRNC cantilever beam to study its electrome-
chanical response, and (3) molecular dynamics (MD)
simulations to determine the mechanical properties of
graphene sheet.
2 Effective piezoelastic properties of GRNC
In this section, the piezoelastic properties of GRNC
were obtained considering a graphene sheet as a
piezoelectric continuum medium. To simplify
123
Effect of flexoelectricity on the electromechanical response
computational efforts, several researchers modeled the
graphene sheet as a continuum plate in order to obtain
its bulk properties (Park et al. 2010; Roberts et al.
2010). Most of the existing studies on the straining of
graphene are based on the analytical as well as
numerical solutions using the concept of continuum
elasticity and hence the graphene can be used as a
continuum medium (Gupta and Batra 2010; Gradinar
et al. 2013; Verma et al. 2014; Bahamon et al. 2015).
This implies that, for a homogeneously deformed
graphene, the displacement of each atom in it is given
by the deformation of the continuum medium, on
which the atom is embedded.
GRNC is assumed to be comprised of piezoelectric
graphene sheets and aluminum matrix. Such
nanocomposite can be considered to be made of
rectangular representative volume elements (RVEs)
containing both graphene sheet and matrix as shown in
Fig. 1, and we confined our micromechanical analysis
to a single RVE. We assumed that the bonding
between the graphene and aluminum matrix is perfect
and the resulting nanocomposite is homogeneous (Gao
and Li 2005; Song and Youn 2006; Jiang et al. 2009;
Kundalwal and Ray 2011, 2013). The upper and lower
surfaces of the GRNC lamina are electroded and the
transverse electric field is applied across them. Hence,
the electric polarization exists in the piezoelectric
medium when it is kept in a parallel plate capacitor
with an electric potential applied across the lamina
even if these parallel plates are not in contact with the
lamina. This is associated with the phenomenon of
converse piezoelectric effect and thus proposed
GRNC lamina may be considered as a capacitor
having two parallel plates in which the graphene and
aluminium matrix act as the dielectric medium. By
using the analytical and numerical micromechanics
models, the effective piezoelastic properties of GRNC
lamina can be obtained.
2.1 Analytical micromechanics models
Figure 1 shows a schematic of RVE of GRNC in
which the graphene is reinforced along the 3–direc-
tion. Assuming the graphene as a solid fiber, the
micromechanical model developed by Kundalwal and
Ray (2011) was modified to determine the elastic
properties of GRNC.
Based on the material coordinate system (1–2–3),
the constitutive relations for the different phases of
GRNC are given by
rrf g ¼ Cr½ � erf g; r ¼ g,m and nc ð1Þ
where the states of stress and stain vectors, and the
elastic coefficient matrix of the rth phase are
rrf g ¼ rr1 rr
2 rr3 rr
23 rr13 rr
12½ �T;erf g ¼ er1 er2 er3 er23 er13 er12½ �T;
Cr½ � ¼
Cr11 Cr
12 Cr13 0 0 0
Cr12 Cr
22 Cr23 0 0 0
Cr13 Cr
23 Cr33 0 0 0
0 0 0 Cr44 0 0
0 0 0 0 Cr55 0
0 0 0 0 0 Cr66
2666666664
3777777775
ð2Þ
In Eqs. (1) and (2), the respective g, m, and nc denote
the graphene, aluminum matrix, and GRNC. The
superscript r is used to denote the respective con-
stituent phases; rr1, r
r2, and r
r3 are the normal stresses
in the direction 1, 2, and 3, respectively; er1, er2, and er3
are the corresponding normal strains;rr12, r
r13, and r
r23
are the shear stresses; er12, er13, and er23 are the
corresponding shear strains; and Crij are the elastic
coefficients of rth phase.
In order to satisfy the perfectly bonding condition
between a fiber and the matrix, researchers mainly
used the iso-field conditions and rules of mixture
(Smith and Auld 1991; Benveniste and Dvorak 1992;
Fig. 1 Cross sections of
RVE of GRNC
123
S. I. Kundalwal et al.
Kundalwal and Ray 2011; Kundalwal 2017). The iso-
field conditions allow us to assume that the normal
strains in a fiber, matrix, and homogenized composite
are equal along the fiber direction while transverse
stresses in the same phases are equal along the
direction transverse to the fiber length. The rules of
mixture allows us to express the normal stress along
the fiber direction and the transverse strains along the
normal to the fiber direction of the homogenized
composite in terms of that in the fiber and matrix as
well as their volume fractions. Such iso-field condi-
tions and rules of mixture for satisfying the perfect
bonding conditions between a graphene and the matrix
can be expressed as
rg1
rg2
eg3rg23
rg13
rg12
8>>>>>><>>>>>>:
9>>>>>>=>>>>>>;
¼
rm1
rm2
em3rm23
rm13
rm12
8>>>>>><>>>>>>:
9>>>>>>=>>>>>>;
¼
rnc1
rnc2
enc3rnc23
rnc13
rnc12
8>>>>>><>>>>>>:
9>>>>>>=>>>>>>;
ð3Þ
and
Vg
eg1eg2rg3
eg23eg13eg12
8>>>>>><>>>>>>:
9>>>>>>=>>>>>>;
þ vm
em1em2rm3
em23em13em12
8>>>>>><>>>>>>:
9>>>>>>=>>>>>>;
¼
enc1enc2rnc3
enc23enc13enc12
8>>>>>><>>>>>>:
9>>>>>>=>>>>>>;
ð4Þ
where vg and vm are the volume fractions of a
graphene and the aluminum metal matrix with respect
to the total volume of RVE of GRNC, respectively;
and vm = 1 - vg. Using Eqs. (1)–(4), the stress and
strain vectors of GRNC can be written in terms of the
corresponding stress and strain vectors of constituent
phases as follows:
rncf g ¼ C1½ � egf g þ C2½ � emf g ð5Þ
encf g ¼ V1½ � egf g þ V2½ � emf g ð6Þ
Also, the relationship between the stresses and strains
in a graphene and the aluminum matrix given by
Eq. (3) can be written as
C3½ � egf g � C4½ � emf g ¼ 0 ð7Þ
The matrices obtained in Eqs. (5)–(7) are given by
C1½ � ¼ vg
0 0 0 0 0 0
0 0 0 0 0 0
Cg13 C
g23 C
g33 0 0 0
0 0 0 0 0 0
0 0 0 0 0 0
0 0 0 0 0 0
2666666664
3777777775;
C2½ � ¼
Cm11 Cm
12 Cm12 0 0 0
Cm12 Cm
11 Cm12 0 0 0
vmCm12 vmC
m12 vmC
m11 0 0 0
0 0 0 Cm44 0 0
0 0 0 0 Cm44 0
0 0 0 0 0 Cm44
2666666664
3777777775;
C3½ � ¼
Cg11 C
g12 C
g13 0 0 0
Cg12 C
g22 C
g23 0 0 0
0 0 1 0 0 0
0 0 0 Cg44 0 0
0 0 0 0 Cg55 0
0 0 0 0 0 Cg66
2666666664
3777777775;
C4½ � ¼
Cm11 Cm
12 Cm12 0 0 0
Cm12 Cm
11 Cm12 0 0 0
0 0 1 0 0 0
0 0 0 Cm44 0 0
0 0 0 0 Cm44 0
0 0 0 0 0 Cm44
2666666664
3777777775;
V1½ � ¼
vg 0 0 0 0 0
0 vg 0 0 0 0
0 0 0 0 0 0
0 0 0 vg 0 0
0 0 0 0 vg 0
0 0 0 0 0 vg
26666664
37777775
and
V2½ � ¼
vm 0 0 0 0 0
0 vm 0 0 0 0
0 0 1 0 0 0
0 0 0 vm 0 0
0 0 0 0 vm 0
0 0 0 0 0 vm
26666664
37777775
ð8Þ
in Eqs. (6) and (7), egf g and emf g are the strain vectorsof a graphene and the aluminum metal matrix,
respectively, and they can be expressed in terms of
GRNC strain vector encf g. Subsequently, using
Eqs. (5)–(7), the states of stresses and strains in
GRNC can obtained as follows:
123
Effect of flexoelectricity on the electromechanical response
rncf g ¼ Cnc½ � encf g ð9Þ
where the effective elastic coefficient matrix Cnc½ � ofthe GRNC is given by
Cnc½ � ¼ C1½ � V3½ ��1þ C2½ � V4½ ��1 ð10Þ
and
V3½ � ¼ V1½ � þ V2½ � C4½ ��1C3½ � ð11Þ
V4½ � ¼ V2½ � þ V1½ � C3½ ��1C4½ � ð12Þ
Using the piezoelastic coefficients of graphene and
matrix, the effective piezoelectric constants of GRNC
can be determined using the existing models (Smith
and Auld 1991; Ray and Pradhan, 2006; Kumar and
Chakraborty 2009). The values of piezoelectric coef-
ficients of a composite material obtained by Smith and
Auld (1991) are larger than that of values determined
by Ray and Pradhan (2006) because of consideration
of iso-strain conditions in both x and y-directions by
former researchers. The effective piezoelectric con-
stant e31 of the GRNC defines the normal stress
induced in transverse x-direction because of the
application of a unit electric field in longitudinal
z-direction. The expression for the effective piezo-
electric constant e31 can be written as follows (Smith
and Auld 1991; Kumar and Chakraborty 2009):
e31 = vge31gðC11m � C12mÞ=ða1 + a2Þ ð13Þ
Similarly, the effective piezoelectric constants e32 and
e33 define the normal stresses induced in respective y-
and z-directions because of the application of a unit
electric field in the longitudinal z-direction. While the
piezoelectric constant e15 quantifies the induced shear
stress about y-direction per unit electric field applied
in the x-direction. The closed form expressions of
various effective piezoelectric constants of GRNC are
given below:
e32 = e32g � ðb1C22g + b2C23gÞ=Q ð14Þ
e33 ¼ vgðe33g � 2vme31gðC13g � C12mÞ=ða1 þ a2ÞÞð15Þ
e15 = e15gð1� vmC55g=ðvgC55m + vmC55gÞÞ ð16Þ
e24 ¼ e24gð1� vmC44g=ðvgC44m þ vmC44gÞÞ ð17Þ
Note that the GRNC is the transversely isotropic
material with the 3-axis as the axis of symmetry;
therefore, e31 ¼ e32 and e24 = e15. Hence, only the
three independent piezoelectric constants (e31; e33; and
e15) are required to study the piezoelectric behaviour
of GRNC. Subsequently, the effective permittivity
constant (233) of GRNC is determined by using the
following expression (Ray and Pradhan 2006):
233¼ vg 233g þvm233m þe31gvgvm=ðvmC11g þ vgC11mÞ ð18Þ
where
Q ¼ vmC22g þ vgC22m
� �vmC33g þ vgC33m
� �
� vmC23g þ vgC23m
� �2 ð19Þ
a1 ¼ vgðC11m þ C12mÞ ð20Þ
a2 ¼ vmðC11g þ C12gÞ ð21Þ
b1 ¼ vme31gðvmC33g þ vgC33mÞ � vme33gðvmC23g
þ vgC23mÞð22Þ
b2 ¼ �vme31gðvmC23g þ vgC23mÞ þ vme33gðvmC22g
þ vgC22mÞð23Þ
2.2 FE modeling of piezoelastic properties
of GRNC
It is important to mention that the micromechanics
models developed in the preceding section are based on
the rules of mixture and iso-field assumptions. Numer-
ical or experimental investigations may be carried out
to verify these assumptions because both the analyses
do not require any such approximations (Kundalwal
and Ray 2012). Therefore, in the current study, FE
models were developed to validate the assumptions
used in Sect. 2.1 by employing the commercial
software ANSYS 15.0. The FE analysis was catego-
rized into the fully coupled electromechanical analysis
in which the modeling of three-dimensional RVE or
unit cellwas carriedwith 20 noded brick element ‘‘solid
226’’ which has both displacement and voltage degrees
of freedom (DOF). Figures 2 and 3 show the RVEs of
123
S. I. Kundalwal et al.
homogenized andFEmeshofGRNC, respectively. The
RVE of GRNC was homogenized and analyzed under
various boundary conditions. FE model of the RVE of
homogenous transversely isotropic GRNCwith its axis
of transverse isotropy being along the graphene was
developed for evaluating the eight independent piezoe-
lastic coefficients: Ceff11 , C
eff12 , C
eff13 , C
eff33 , C
eff44 ; e
eff13 , e
eff15
and eeff33 . The effective piezoelastic coefficients of the
GRNC can be determined by applying the appropriate
boundary conditions to the RVE to be discussed in
subsequent sections.
The combined electromechanical relations of
GRNC are given by Eq. (24) in which Ceffij , e
effij , and
2effij are the effective elastic constants, piezoelectric
constants and permittivity constants of GRNC,
respectively.
Under the conditions of an imposed electrome-
chanical loads on the RVE of GRNC, the average
stress rij
� �, strain eij
� �, electrical displacement Di
� �
and electric field Ei
� �are defined as below
rij
� �¼ 1
V
Z
v
rij
� �dV; eij
� �¼ 1
V
Z
v
eij� �
dV
Di
� �¼ 1
V
Z
v
Dif gdV; Ei
� �¼ 1
V
Z
v
Eif gdV ð25Þ
where v represents the volume of the GRNC RVE and
the quantity with an overbar represents the volume
averaged quantity. It is evident from Eq. (24) that if at
any point in the GRNC only one normal strain is
present while the other strain components are zero
then three normal stresses exists. The ratio between
any one of these three normal stresses and the normal
strain yields an effective elastic coefficient. Thus,
three such elastic coefficients at the point can be
calculated with one numerical experiment. Hence, the
determination of a particular effective piezoelastic
coefficient from the FE model needs to prescribe the
appropriate boundary conditions on the faces of the
GRNC RVE.
2.2.1 Effective elastic coefficients Ceff13 and C
eff33
In order to compute the effective elastic constants
Ceff13 and Ceff
33 of the GRNC, the RVE shown in Fig. 4
can be deformed in such a way that the normal strain
e33 is only present in it while all other strain
components are zero. In order to achieve such states
of strain, displacements at the five boundary surfaces
ðx1 ¼ 0 and a; x2 ¼ 0 and b; x3 ¼ 0Þ need to pre-
scribed to zero (e11 ¼ e22 ¼ e23 ¼ e13 ¼ e12 ¼ 0Þ. Itshould be noted that x1; x2; and x3 denote the coor-
dinates corresponding to 1, 2, and 3-axes, respectively.
A uniform normal displacement (u3) along the 3-
direction needs to be applied on the surface (x3 ¼ l) of
the RVE such that it is subjected to e33 only. Likewise,the electric fields (voltage DOF) at all faces are
required to constrain to zero (E1 ¼ E2 ¼ E3 ¼ 0).
Using Eq. (25), the average stresses and strains
(r11;r33; and e33) can be obtained. Then, the values
of effective elastic coefficients textCeff33 ð¼ r33=e33Þ
and Ceff13 ð¼ r11=e33Þ can be determined using Eq. (24)
for different volume fractions of graphene. Figure 4
shows the stress and strain distributions in the RVE
obtained along the graphene direction.
r11
r22
r33
r23
r13
r12
D1
D2
D3
8>>>>>>>>>>>>>>>><>>>>>>>>>>>>>>>>:
9>>>>>>>>>>>>>>>>=>>>>>>>>>>>>>>>>;
¼
Ceff11 Ceff
12 Ceff13 0 0 0 0 0 � eeff31
Ceff12 Ceff
22 Ceff13 0 0 0 0 0 � eeff31
Ceff13 Ceff
13 Ceff33 0 0 0 0 0 � eeff33
0 0 0 Ceff44 0 0 0 � eeff15 0
0 0 0 0 Ceff55 0 � eeff15 0 0
0 0 0 0 0 Ceff66 0 0 0
0 0 0 0 eeff15 0 2eff11 0 0
0 0 0 eeff15 0 0 0 2eff22 0
eeff31 eeff31 eeff33 0 0 0 0 0 2eff33
266666666666666664
377777777777777775
e11e22e33e23e13e12E1
E2
E3
8>>>>>>>>>>>>>>>><>>>>>>>>>>>>>>>>:
9>>>>>>>>>>>>>>>>=>>>>>>>>>>>>>>>>;
ð24Þ
123
Effect of flexoelectricity on the electromechanical response
2.2.2 Effective elastic coefficients Ceff11 and Ceff
12
In order to determine the effective elastic coefficients
Ceff11 and Ceff
12 of GRNC, the RVE needs to be imposed
to the states of strain such that only normal strain e11 ispresent while all other strain components are zero
(e22 ¼ e33 ¼ e23 ¼ e13 ¼ e12 ¼ 0Þ: Such states of
strain can be attained by constraining the surfaces of
RVE in the following manner:
u1 ¼ 0 at x1 ¼ 0; u2 ¼ 0 at x2 ¼ 0 and b; u3 ¼ 0 at
x3 ¼ 0 and 1.
In the same way, the electric field at all surfaces of
RVE are required to constrain to zero
(E1 ¼ E2 ¼ E3 ¼ 0). Due to the essential boundary
conditions, the uniform normal displacement (u1) is
required to apply on the surface x1 ¼ a of the RVE
such that it is under the application of e11 only. Using
Eqs. (24) and (25), the average stresses and strain
(r11;r22 and e11) can be obtained to calculate the
values of Ceff11 ð¼ r11=e11Þ and Ceff
12 ð¼ r22=e11Þ. Thedistributions of stresses and strains are shown in Fig. 5
when the deformation is applied to the RVE in the
transverse direction to the length of graphene.
2.2.3 Effective piezoelastic coefficients
Ceff44 ; e
eff15 and Ceff
66
To estimate the effective elastic coefficient Ceff44 of
GRNC, an out-of-plane shear in the x1–x3 plane of the
RVE is required to subject the pure shear deformation
in such a way that the shear strain e23 is non-zero whilethe remaining strain components are zero. Such states
of strain can be achieved by prescribing the surface
given by x3 ¼ 0 of the RVE and imposing the uniform
distributed tangential force on the surface given by
x3 ¼ l. In the same way, the electric potential at all
surfaces of the RVE are required to constrain to zero
(E1 ¼ E2 ¼ E3 ¼ 0). Subsequently, the average shear
stress and strain (r23 and e23Þ induced in the RVE can
be determined using Eq. (25). Finally, the effective
elastic coefficient Ceff44 can be estimated using relation:
r23=e23. Note that the effective elastic coefficients Ceff66
is not independent elastic coefficient and it can be
computed directly from the relation Ceff11 � Ceff
12
� �=2.
In order to calculate the effective piezoelectric
coefficient eeff15 , the boundary conditions similar to
obtain Ceff44 can be used such that the RVEwas imposed
to shear strain e23 only ðe11 ¼ e22 ¼ e33 ¼ e13 ¼e12 ¼ 0Þ and electric potential needs to be constrainedto zero on the two surfaces of RVE (E1 ¼ E2 ¼ 0).
Using Eq. (24), the values of eeff15 can be calculated
using the ratio eeff15 ¼ D2=e23 for different volume
fractions of graphene. Figure 6 depicts the distribu-
tions of out-of-plane shear stresses and strains in the
RVE of GRNC.
2.2.4 Effective piezoelectric and permittivity
coefficients eeff33 ; e
eff13 and ε
eff33
The effective piezoelectric coefficients eeff13 and eeff33 are
proportional to the in-plane and out-of-plane actua-
tions of piezoelectic materials, respectively. In order
to determine the values of eeff13 ; eeff33 ; and permittivity
Fig. 2 Homogenized RVE of GRNC
Fig. 3 FE mesh of the RVE of GRNC
123
S. I. Kundalwal et al.
constant εeff33 , converse to the boundary conditions of
Ceff33 and Ceff
13 , all the surfaces of RVE are required to
constrain so that their normal displacements are zero
ðe11 ¼ e22 ¼ e33 ¼ e23 ¼ e13 ¼ e12 ¼ 0Þ. The
uniform electric potential needs to apply to the RVE
in 3-direction and its remaining surfaces are required
to constrain to zero electric potentials (E1 ¼ E2 ¼ 0).
Figure 7 illustrates the distributions of electric
Fig. 4 FE simulations
showing distributions of astrain e33 and b stress r33 in
the RVE
Fig. 5 FE simulations
showing distributions of astrain e11 and b stress r11 in
the GRNC RVE
Fig. 6 FE simulations
showing distributions of ashear strain ðc23Þ and bshear stress ðs23Þ in the
GRNC RVE
123
Effect of flexoelectricity on the electromechanical response
displacement and electric potential in the RVE.
Subsequently, the average values of r11, r33, D3 and
E3 can be computed using Eq. (25). Then, using
Eq. (24), the effective values of eeff33 , eeff13 and ε
eff33 can be
evaluated using the respective ratios �r33=E3,
�r11=E3, and �D3=E3.
3 Piezoelasticity model of GRNC cantilever beam
Tremendous research on nanocomposite structures has
been carried out in the last decade with the aim of
developing NEMS. Among all structural elements,
piezoelectric composite cantilever beams have found
wide applications such as sensors, transducers and
actuators in NEMS. Therefore, here an attempt was
made to show the potential of cantilever beammade of
flexoelectric GRNC in which strain gradient is incor-
porated using its effective piezoelastic properties
obtained in previous sections. The generalized equa-
tion for the internal energy density function can be
written as follows (Shen and Hu 2010):
U ¼ 1
2bklPkPl þ
1
2Cijkleijekl þ dijkeijPk þ fijklui;jkPl
þ rijklmeijuk;lm þ 1
2gijklmnui;jkul;mn
ð26Þ
where Pi and ui are the components for polarization
and displacement vector, while ei are the components
for strain vectors. Cijkl, dijk, and bkl are the fourth orderelastic coefficient, third order of piezoelectric
coefficient and second order tensor of reciprocal
dielectric susceptibility, respectively. fijkl is the fourth
order flexoelectric coefficient tensor, while gijklmn are
the elements for purely nonlocal elastic effects and
related to strain gradient elastic theories and rijklmrepresent strain and strain gradient coupling tensors.
The strain vector is defined as
eij ¼1
2
oui
oxjþ ouj
oxi
� �ð27Þ
For the sake of simplicity, the elements gijklmn and
rijklm are assumed to be zero. Hence, the constitutive
equations can be expressed as
rij ¼oU
oeij¼ Cijklekl þ dijkPk ð28aÞ
sijm ¼ oU
oui;jm¼ fijmkPk ð28bÞ
Ei ¼oU
oPi¼ bijPj þ djkiejk þ fjkliuj;kl ð28cÞ
where rij, Ei, and sijm are the Cauchy stress tensor, the
electric field, and the moment stress or the higher order
stress, respectively. In higher order stress, sijm is
induced by the flexoelectric effect while it does not
present in the classical theory of piezoelectricity. The
various tensorial terms in Eq. (28) are given by
Fig. 7 FE simulations
showing the distributions of
a electric displacement ðD3Þand b electric potential ðE3Þin the GRNC RVE
123
S. I. Kundalwal et al.
rx
ry
rz
ryz
rxz
rxy
8>>>>>>>><>>>>>>>>:
9>>>>>>>>=>>>>>>>>;
¼
C11 C12 C13 0 0 0
C12 C22 C23 0 0 0
C13 C23 C33 0 0 0
0 0 0 C44 0 0
0 0 0 0 C55 0
0 0 0 0 0 C66
2666666664
3777777775
exeyez2eyz2exz2exy
8>>>>>>>><>>>>>>>>:
9>>>>>>>>=>>>>>>>>;
þ
d11 d21 d31
d12 d22 d32
d13 d23 d33
d14 d24 d34
d15 d25 d35
d16 d26 d36
2666666664
3777777775
Px
Py
Pz
8><>:
9>=>;
ð29aÞ
Ex
Ey
Ez
8><>:
9>=>;
¼ �d11 d12 d13 d14 d15 d16
d21 d22 d23 d24 d25 d26
d31 d32 d33 d34 d35 d36
264
375
exeyez2eyz2exz2exy
8>>>>>>>><>>>>>>>>:
9>>>>>>>>=>>>>>>>>;
þb11 0 0
0 b22 0
0 0 b33
264
375
Px
Py
Pz
8><>:
9>=>;
ð29bÞ
A schematic of GRNC cantilever beam is shown in
Fig. 8 which has width b, length L and height h,
referred to the Cartesian coordinate system x–z.
A GRNC cantilever beam is considered to be made
of graphene and aluminum metal matrix. The arrange-
ment of graphene and aluminum matrix layers can be
varied to obtain a different volume fraction of graphene
for the piezoelectric analysis. Here, the thickness of
each single graphene layer was taken as 0.34 nm (Alian
et al. 2015a, b, 2017; Kundalwal and Meguid 2017).
The piezoelectric GRNC cantilever beam is polar-
ized along the z-axis. A constant concentrated load is
applied at the free end (x ¼ L) of cantilever beam and
a constant voltage V is applied between the upper and
lower surfaces of beam i.e., at z ¼ þ h2and z ¼ � h
2,
respectively. If the w xð Þ is the transverse displacement
of bending of the beam then using Euler beam
hypotheses the axial displacement at any point in it
is given as (Yan and Jiang 2013)
u x; zð Þ ¼ u0 xð Þ � zdw xð Þdx
ð30Þ
where u0 xð Þ is the axial displacement along the
longitudinal axis of the beamwhich may be introduced
by mechanical and electric loads due to the elec-
tromechanical coupling or flexoelectric effect. Using
Eq. (27), the non-zero strain can be written as
ex ¼du0
dx� z
d2w
dx2ð31Þ
Here, the thickness of a cantilever beam is considered
as very small as compared to its length ðh � LÞ.Hence one can assume that transverse displacement of
a cantilever beam is greater as compared to its
longitudinal displacement. Therefore, strain gradient
ex;x ¼ d2u0
dx2 � z d3w
dx3 can be omitted because it is negli-
gible as compared to ex;z ¼ � d2w
dx2. Therefore for
further formulation, we only considered strain gradi-
ent � d2w
dx2, which is induced by the flexoelectricity.
Fig. 8 schematic of GRNC
cantilever beam
123
Effect of flexoelectricity on the electromechanical response
We can formulate the electric field (EzÞ consideringit is only present in the z-direction ðEx ¼ Ey ¼ 0Þ(Ying and Zhifei 2005) and it can be calculated against
the variation of the thickness of beam corresponding to
the constant electrical potential. From Eqs. (28c) and
(30), the electric field in thickness direction is given by
Ez ¼ b33Pz þ d31ex þ f13ex;z ð32Þ
The extra term f13ex;z in the above equation is differentfrom the theory of linear piezoelectricity which
contributes to the flexoelectric effect. For a complete
formulation of the problem, in the absence of body
charges, the Gauss’ law is expressed as
ε0o2uoz2
þ oPz
oz¼ 0 ð33Þ
The relationship between the internal energy density
function and electric enthalpy density function can be
defined as (Shen and Hu 2010)
H ¼ U� 1
220 u;zu;z þ u;zPz ð34aÞ
where ε0 ¼ 8:85� 10�12 C=V m is the permittivity of
free space or vacuum. The relation between an electric
potential (u) and the electric field (Ez) is given by
Ez ¼ �u;z ð34bÞ
With consideration of the electric boundary condition
uðh=2Þ ¼ V and uð�h=2Þ ¼ 0, the polarization (Pz)
and electric field (Ez) from Eqs. (32) and (33) can be
written in terms of u0; and w as follows
Pz ¼20 d31
20 b33 þ 1zd2w
dx2� d31
b33
du0
dxþ f13
b33
d2w
dx2� V
b33h
ð35Þ
Ez ¼ � d31
20 b33 þ 1zd2w
dx2þ V
h
� �ð36Þ
By substituting Eq. (35) into Eq. (28a), the axial stress
(rx) can be determined as
rx ¼ C11 �d231b33
� �du0
dx� C11 �
20 d231
20 b33 þ 1
� �zd2w
dx2
þ d31f13
b33
d2w
dx2� d31V
b33h
ð37Þ
Using Eq. (37), the axial force ðFxÞ can be determined
as follows
Fx ¼ r
h2
�h2
rxdz
¼ bh C11 �d231b33
� �du0
dxþ d31f13
b33
d2w
dx2� d31V
b33h
�
ð38Þ
By simplifying Eq. (38), we can obtain
bh C11 �d231b33
� �du0
dxþ d31f13
b33
d2w
dx2� d31V
b33h
� ¼ 0
ð39aÞ
� C11 �d231b33
� �du0
dx¼ d31f13
b33
d2w
dx2� d31V
b33hð39bÞ
Because of the absence of external body forces and
mechanical loads in the axial direction, the relaxation
strain in the cantilever beam is present which plays
important role in its softer and stiffer behavior. The
relaxation strain can be defined as
du0
dx¼
� C11 � d231b33
�
d31f13b33
d2w
dx2 � d31V
b33h
� ð40Þ
The governing equation of piezoelectric nanobeams
including the effect of flexoelectricity is obtained
using the energy method. Using Eqs. (26), (28), and
(34b), the internal energy density function can be
written as
U ¼ 1
2rxex þ sxxzex;z � u;zPz� �
ð41Þ
in which,
sxxz ¼20 d31f13
20 b33 þ 1zþ f 213
b33
� �d2w
dx2� d31f13
b33
du0
dx� Vf13
b33h
�
ð42Þ
123
S. I. Kundalwal et al.
Next, variational principle can be formulated over
the entire volume of the GRNC piezoelectric beam and
can be written as (Mindlin 1968):
�dZ
V
HdVþ dW ¼ 0 ð43Þ
Subsequently, the governing equations of GRNC
piezoelectric cantilever beam can be obtained as
follows
C11 �d231b33
� �bh
d2u0
dx2þ d31f13bh
b33
� �d3w
dx3¼ 0 ð44aÞ
C11 �20 d
231
20 b33 þ 1
� �bh3
12� f213bh
b33
� �d4w
dx4
þ d31f13bh
b33
� �d3u0
dx3
¼ 0 ð44bÞ
For the cantilever beam, the transverse displacement
and slope can be obtained using the following
boundary conditions
wjx ¼ 0;dw
dx
����x ¼ 0 ð45Þ
The moment and force at x = L become:
C11 �20 d
231
20 b33 þ 1
� �bh3
12� f213bh
b33
� �d2w
dx2
þ d31f13bh
b33
� �du0
dxþ f13Vb
b33¼ 0 ð46aÞ
� C11 �20 d
231
20 b33 þ 1
� �bh3
12� f213bh
b33
� �d3w
dx3
� d31f13bh
b33
� �d2u0
dx2þ F
¼ 0 ð46bÞ
where the first terms in above equations are the
effective bending rigidity considering the flexoelectric
effect. Substituting the boundary conditions
0� x�Lð Þ in governing Eqs. (46a) and (46b) of
GRNC cantilever beam, the transverse deflection can
be obtained as follows
wcantilever ¼Px2
6 EIð Þcantileverx� 3Lð Þ
� C11f13Vbx2
2 b33C11 � d231� �
EIð Þcantileverð47aÞ
In absence of flexoelectricity effect (f13 ¼ 0),
Eq. (47a) gets reduced to
wcantilever ¼Px2
6 EIð Þcantileverx� 3Lð Þ ð47bÞ
where,
EIð Þcantilever ¼ C11 �20 d
231
20 b33 þ 1
� �bh3
12� f213bh
b33
� d231f213bh
b33ðb33C11 � d231Þ
ffi C11 �20 d
231
20 b33 þ 1
� �bh3
12� f213bh
b33
4 Elastic properties of graphene
In order to estimate the effective piezoelastic proper-
ties of the GRNC, the elastic properties of graphene
are required first. Therefore, we first determined the
elastic properties of graphene sheet using MD simu-
lations. It is the the most widely used tools in the
theoretical study of nanostructures and it calculates the
time-dependent behaviour of a molecular system and
permits accurate property predictions via accounting
interactions between atoms and molecules at the
atomic level (Shah and Batra 2014b; Alian et al.
2015a, b; Kundalwal and Meguid 2017; Kothari et al.
2018). This serves a complement to conventional
experiments with cheaper and faster simulations. All
MD simulations runs were conducted with large-scale
atomic/molecular massively parallel simulator
(LAMMPS) (Plimpton 1995), and the molecular
interactions in graphene were described in terms of
Adaptive Intermolecular Reactive Empirical Bond
Order (AIREBO) force fields (Stuart et al. 2000).
The systematic steps followed in the MD simula-
tions are as follows. First, the intial structure of
graphene was prepared. Then, simulations were
started with an energy minimization using a conjugate
gradient method to obtain the optimized structure of
graphene. A graphene was considered as optimized
123
Effect of flexoelectricity on the electromechanical response
structure when the total potential energy between
adjacent steps was less than 1.0 9 10-10 kcal/mol.
Simulation in each case was performed in the constant
temperature and volume conical (NVT) ensemble
using a time step of 0.5 fs with the total time of 50 ps
to equilibrate the graphene structure, where the
velocity Verlet algorithm was used to integrate
Newton’s classical equations of motion. In the present
work, the load was applied to a graphene sheet and
then the energy was computed as the result of
interatomic interactions of neighbouring atoms. The
stress of the graphene sheet was computed by aver-
aging the obtained stress of each carbon atom in it.
Then, the stress–strain curve during tensile loading
was obtained and Young’s modulus (E) and Poisson’s
ratio (l) of graphene sheet were determined. The
determination of values of E and l a graphene layer
was accomplished by using the strain energy density-
elastic constant relations (Kundalwal and Choyal
2018). The equivalent continuum graphene sheet
was assumed to be a flat plate considering its wall
thickness of 3.4 A (Alian et al. 2015a, b, 2017;
Kundalwal andMeguid 2017). A direct transformation
to continuum properties was then made by assuming
that the potential energy density of discrete atomic
interactions of neighbouring atoms is equal to the
strain energy density of the continuous substance
occupying a graphene volume. The atomic volume
was determined from the relaxed graphene sheet with
the thickness of 3.4 A.
5 Results and discussions
As a first endeavor, MD simulations were carried out
to determine the elastic properties of graphene sheet.
The predicted values of E and l are summarized in
Table 1, and they agree well with the results obtained
by other researchers using different modeling tech-
niques and potentials as well as experimental esti-
mates (Lee et al. 2008; Zhang et al. 2012; Dewapriya
et al. 2015).
Next, the effective piezoelastic coefficients of
GRNC were evaluated using two different models
developed in Sect. 2. Then, the obtained effective
piezoelastic coefficients of GRNC were used to
study the electromechanical response of GRNC
cantilever beam. A concentrated force P = 1 nN
was applied at the end of GRNC cantilever beam
having width, b ¼ h, and length, l ¼ 20h. We
considered permittivity of graphene same as that of
graphite, 211¼233¼ 1:106� 10�10 F=m (Munoz-
Hernandez et al. 2017). Usually, the fiber volume
fraction in the composite varies considerably accord-
ing to the manufacturing route, typically from 0.2 to
0.7. Therefore, we calculated the piezoelastic proper-
ties of GRNC for different volume fractions of
graphene, from 0.2 to 0.7. Since the GRNC is
transversely isotropic with 3-axis as the axis of
symmetry, only the five independent effective elastic
coefficients of GRNC (C11, C12, C13, C33 and C44) are
presented here. Figure 9 illustrates the variation of the
effective axial elastic coefficient C33 of the GRNC
with the graphene volume fraction. It may be observed
that the value of C33 increases almost linearly with the
graphene volume fraction. This result is coherent with
the previously reported results for graphene based
nanocomposites (Zhao et al. 2010; Khan et al. 2012; Ji
et al. 2016; Garcıa-Macıas et al. 2018). Almost 100%
agreement between the two sets of the values of C33
estimated by the MOM and FE models ensures the
validity of the assumptions and the rules of mixture for
deriving the MOMmodel. Note that the effective axial
elastic coefficient (C33) was estimated considering the
Table 1 Properties of graphene and aluminium matrix
Material E(GPa) l e31 (C/m2) e33 (C/m2) e15 (C/m2) 233 (F/m)
Graphene 985 (Present) 0.26 (Present) - 0.221 Kundalwal
et al. (2017)
0.221 Kundalwal
et al. (2017)
- 0.221 Kundalwal
et al. (2017)1.106 �10�10
Munoz-Hernandez
et al. (2017)
Aluminum 70 (Scari
et al. 2014)
0.33 (Scari
et al. 2014)
– – – 1.504 �10�11
Sundar et al.
(2016)
123
S. I. Kundalwal et al.
iso-strain condition along the graphene direction and
hence such estimation belongs to the Voigt-upper
bound.
Figure 10 demonstrates the variation of the effec-
tive elastic coefficient C13 of the GRNC with the
graphene volume fraction. The MOM model overes-
timates the value of C13 as compared to the FE
Fig. 9 Variation of the
effective elastic coefficient
C33 of the GRNC with the
graphene volume fraction
Fig. 10 Variation of the
effective elastic coefficient
C13 of the GRNC with the
graphene volume fraction
123
Effect of flexoelectricity on the electromechanical response
estimates. This is attributed to the fact that the
Poisson’s effect was modeled appropriately in the
FE simulations. Extension-extension coupling occurs
between the dissimilar normal stress (r33) and normal
strain (e11) due to the applied load along the axis of
symmetry (i.e., 3-axis). Since the GRNC is
Fig. 11 Variation of the
effective elastic coefficient
C11 of the GRNC with the
graphene volume fraction
Fig. 12 Variation of the
effective elastic coefficient
C12 of the GRNC with the
graphene volume fraction
123
S. I. Kundalwal et al.
transversely isotropic with 3-axis as the axis of
symmetry, the values of C23 of the GRNC are found
to be identical to those of C13 and for brevity are not
presented here.
Figures 11 and 12 demonstrate the variation of
effective elastic coefficients C11 and C12 with the
graphene volume fraction. It may be observed from
Figs. 11 and 12 that the MOM model overestimates
Fig. 13 Variation of the
effective elastic coefficient
C44 of the GRNC with the
graphene volume fraction
Fig. 14 Variation of the
effective permittivity
coefficient 233 of the GRNC
with the graphene volume
fraction
123
Effect of flexoelectricity on the electromechanical response
the respective values of C11 and C12 over that of FE
predictions, especially at larger volume fractions of
graphene. This is due to the fact that the transverse
elastic properties of composites are usually the
function of properties of matrix material and the
predictions of both models are well agreed at lower
volume fractions of graphene. As expected, the
predictions by both models differ significantly as the
graphene volume fraction increases. The values of C22
Fig. 15 Variation of the
effective piezoelectric
coefficient e33 of the GRNC
with the graphene volume
fraction
Fig. 16 Variation of the
effective piezoelectric
coefficient e31 of the GRNC
with the graphene volume
fraction
123
S. I. Kundalwal et al.
of the GRNC are found to be identical to those of C11
but they are shown here for brevity.
Figure 13 demonstrates the variation of effective
elastic coefficient C44 with the graphene volume
fraction. Once again, the MOM model overestimates
the values of C44 over that of FE predictions,
especially at larger volume fractions of graphene.
This finding is coherent with the previously reported
results by Pettermann and Suresh (2000). They
reported that the analytical predictions of only the
longitudinal shear modulus with respect to the elastic
behavior of piezoelectric composite can be altered
significantly compared to the experimental findings.
Figures 14 and 15 demonstrate the variation of
effective permittivity 233 and piezoelectric coefficient
e33 with the graphene volume fraction. Both figures re-
veal that the values of 233 and e33 increased linearly as
the graphene volume fraction increases. Moreover, it
may be observed from this comparison that the two
sets of results are in excellent agreement validating the
analytical micromechanics model used herein. This is
attributed to the imposition of electric potential (volt
DOF in case of FE simulations) in the fiber direction.
Figure 16 illustrates the variation of effective piezo-
electric coefficient e31 of GRNC with the graphene
volume fraction. It may be observed from this
figure that the magnitude of e31 increases with the
graphene volume fraction. Figure 16 clearly shows a
good correlation between the analytical and FE
predictions at wide range of volume fractions of
graphene. Figure 17 demonstrates the variation of
effective piezoelectric coefficient e15 with the gra-
phene volume fraction. This figure shows that that the
magnitude of e15 increases with the graphene volume
fraction as found in case of e31. It may also be observed
from Fig. 17 that the predictions of both models are
well agreed at lower volume fractions of graphene.
Compared to other piezoelectric coefficients, the
predictions of e15 are found to more sensitive to the
larger volume fractions of graphene and this is
attributed to the consideration of boundary conditions
and in-plane behavior of GRNC; the same were
attributed to the variation of values of C44 as shown in
Fig. 13. The research works by Odegard (2004) and
Moreno et al. (2009) also reported the discrepancy in
the predictions of values of e15. Comparison of the
predictions of analytical micromechanics approaches
with that by the FE simulations reveals that the former
models yield conservative estimates of the piezoelas-
tic constants of the GRNC. Hence, predictions by the
analytical micromechanics approaches were consid-
ered in the subsequent section for investigating the
Fig. 17 Variation of the
effective piezoelectric
coefficient e15 of the GRNC
with the graphene volume
fraction
123
Effect of flexoelectricity on the electromechanical response
Fig. 18 Deflection of
GRNC cantilever beam
along its length with
different graphene volume
fractions at V = – 1 V
Fig. 19 Deflection of
GRNC cantilever beam
along its length with
different graphene volume
fractions at V = – 5 V
123
S. I. Kundalwal et al.
effect of flexoelectricity on the electromechanical
response of GRNC cantilever beam.
So far, the effective piezoelastic properties of
GRNC have been determined. To investigate the
effect of flexoelectricity on the electromechanical
response of GRNC cantilever beam, three discrete
values of graphene volume fractions (vg) are consid-
ered as 0.4, 0.6, and 0.8, and the electrical potentials
are considered as - 1 V, - 5 V, and - 10 V.
Figures 18, 19 and 20 illustrate the effect of flexo-
electricity on the GRNC cantilever beam for different
graphene volume fractions and electric potentials. In
our simulations, negative electric potential was
applied over the surface of the GRNC cantilever
beam. These results reveal that the effective bending
rigidity of the GRNC cantilever beams with consid-
eration of the flexoelectricity (f13 6¼ 0) is higher than
that of neglecting flexoelectric effect (f13 = 0). Con-
versely, as positive electric potential (? V) was
applied to the cantilever beam, the softer elastic
behavior exhibited by it when the effect of flexoelec-
tricity (f13) was taken into account; then, induced
inhomogeneous boundary conditions to the bending
behaviour of GRNC cantilever beam were found
exactly opposite to its effective bending rigidity.
Inhomogeneous boundary condition is nothing but the
addition of positive and negative relaxation moments
according to the applied negative and positive electric
potentials, respectively. Thus, it can be concluded that
the stiffer and softer elastic behaviour of GRNC
cantilever beam can be altered by varying electric
potential (± V) and it may find wide applications in
NEMS. In may be observed from Fig. 18, 19 and 20
that the responses of GRNC cantilever beams improve
as the values of volume fraction of graphene and
applied electrical potential are increased. This is
attributed to the fact that the (1) effective piezoelastic
properties of GRNC increase with the increase in
graphene volume fraction in it as shown in Figs. 9, 10,
11, 12, 13, 14, 15, 16 and 17, and (2) flexoelectric
effect enhances as the applied electrical potential
increases. From the above discussion, it may be
observed that the deflections of GRNC cantilever
beam remarkably influenced by the electromechanical
loadings and strain gradients effects.
Fig. 20 Deflection of
GRNC cantilever beam
along its length with
different graphene volume
fractions at V = – 10 V
123
Effect of flexoelectricity on the electromechanical response
6 Conclusions
As the first of its kind, this study reports the effective
piezoelectric and elastic (piezoelastic) properties of
the graphene reinforced nanocomposite material
(GRNC). The mechanics of materials (MOM) and
finite element (FE) models were developed to predict
the effective piezoelastic properties of GRNC using
the piezoelectric graphene. A few MD simulations
were also carried out to determine elastic properties of
a graphene. The calculated piezoelastic properties
were then used to a case study of cantilever beam
made of GRNC for investigating its electromechanical
response. For this purpose, an analytical beam model
was derived using the extended linear piezoelectricity
and Euler beam theories incorporating the flexoelec-
tricity effect. Specific attention was given to investi-
gate the effect of graphene volume fraction and
electrical load. Our results demonstrate that the
flexoelectricity has significant effect on the electrome-
chanical response GRNC beam with mere use of 40%
volume fraction of graphene. It is revealed that the
electromechanical response GRNC cantilever beam is
improved with the increase in the graphene volume
fraction and it can be tuned via applying different
electric potentials. The current results are significant,
which revealed that the flexoelectric phenomena in
graphene induced due to the strain gradient can be
exploited to form next generation NEMS for various
multifarious applications.
Acknowledgements The authors gratefully acknowledge the
financial support provided by the Indian Institute of Technology
Indore and the Science Engineering Research Board (SERB),
Department of Science and Technology, Government of India.
S.I.K. acknowledges the generous support of the SERB Early
Career Research Award Grant (ECR/2017/001863).
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