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performance battery grade material is required. It must have high ionic
conductivity, good redox active nature and high specific surface area.
Furthermore, the stable nature of the electrode is also an important
factor as the battery type electrode possess fewer electrochemical sta
bility due to excessive redox reactions. So, the optimization of efficient
battery grade electrode material with flashing electrochemical perfor
mance like superior specific capacity and high stable nature is needed to
be addressed.
So far, various types of electrode materials like metal oxides, phos
phates, sulfides, and conducting polymers have been used in super
capattery device. Recently, the conducting polymers (CPs) are found as
profitable electrode material for energy storage devices [27–29]. Apart
from the excellent conductivity of CPs, the poor capacity retention and
cyclic stability limit their scope in supercapattery devices [30].
Whereas, metal oxides like ruthenium, iron, and cobalt oxide arise as
useful electrode material for energy storage devices [16,31]. These
materials have a high surface to volume ratio and aggregate when used
in their pure form. The electroactive sites in the material reduce due to
aggregation and it results in dwindling specific capacity [31]. On the
other hand, various metal phosphates like nickel, manganese, and cobalt
phosphates have indicated good conductivity and environment friendly
nature [32,33]. Therefore, due to the fast ion transport mechanism,
these metal phosphates are found to be suitable electrode material for
supercapacitor applications. Nevertheless, the optimization of electrical
conductivity, bandgap, structural flexibility, and carrier mobility are
some of the critical issues need to be solved [32,34,35]. To address these
issues, the use of various nano heterostructures could be the possible
choice. The formation of redox active sites and defects in grain bound
aries of heterostructure result in high ionic conductivity, short diffusion
path and enhanced redox activity. Therefore, extensive research has
been made for the utilization of doped heterostructures of metal phos
phates as battery grade electrode material for hybrid energy storage
devices [35–40]. Jikui et al. [41] utilized 2D porous Co3O4 nano-sheet as
battery grade electrode synthesized via direct hydrothermal method.
The supercapattery device was assembled by using Co3O4 nano-sheets
and AC. The device yields a maximum energy density of 22.49
Whkg− 1
at corresponding power of 800 Wkg-1
with an excellent cyclic
stability of 91.8% after 10,000 GCD cycles. Similarly, Xiaoying et al.
[42] has made composite of battery type MnCoO4 with AC and utilized it
as electrode material for supercapattery device. The composite yields a
maximum specific capacity of 443.5 Cg-1
at 0.5 Ag-1
. Wang et al. [43]
utilize magnesium cobaltite micro flowers (MgCo2O) as battery type
electrode material for supercapattery device. The electrode demonstrate
a maximum specific capacity of 313.3 Cg-1
at 1 Ag-1
in three electrode
assembly. The electrode also demonstrate a cyclic stability of 74.5%
after 5000 cycles. Anjon et al. [44] utilized Urchin-like NiO nanosphere
synthesized via microwave assisted hydrothermal technique as elec
trode material for supercapacitor and batteries. The material is utilized
as anode in lithium ion batteries and it exhibited a specific capacity of
1027 mAhg− 1
and also delivers a specific capacitance of 736 Fg-1
when
used as electrode in supercapacitor. Mirghni et al. synthesized NiCo
(PO4)3/GF based heterocomposite for hybrid supercapacitor. The
fabricated device yields specific energy of 34.8 Whkg− 1
and specific
power of 377 Wkg-1
at 0.5 Ag-1
[45]. Cobalt phosphates are excessively
utilized as electrode material in high performance SC devices. Chen et al.
reported the nano-flower shaped CoP electrode for high performance SC
exhibiting a maximum capacitance of 418 Fg-1
at 1 Ag-1
[46]. The spe
cific energy and specific power are observed to be 8.8 Whkg− 1
and 6
Wkg-1
, respectively, with good cyclic durability of 97% for 6000 cycles.
Furthermore, J. Zhao et al. performed the hydrothermal synthesis of
ammonium nickel phosphate hydrate and used it for supercapacitor
applications [47]; a maximum capacitance of 1072 Fg-1
at 1.5 Ag-1
in
three cell assembly and the device showed a good cyclic stability of 95%
after 3000 GCD cycles. Liu et al. fabricated a mixed metal phosphate
composite by using a microwave synthesis technique [48]. The electrode
displayed the highest capacitance of 828 Fg-1
at 1 Ag-1
with 81.3%
capacitance retention after 3000 cycles.
Here, we synthesized nickel-manganese phosphate via sono-
chemical method as a working electrode in supercapattery devices.
The binary composites are made by mixing Mn and Ni in equal ratios and
calcined at 400 ◦
C to test for energy storage applications. Electro
chemical measurements like CV, GCD, and EIS are performed in three-
electrode assembly; an electrode with the best electrochemical perfor
mance was used in supercapattery device. Our device comprised of
NiMn(PO4)2 and activated carbon as positive and negative electrodes,
respectively. This asymmetric device is tested in two electrode assembly.
The electrochemical results reveal high specific energy of 64.2 Whkg− 1
and a maximum specific power of 11,896 Wkg-1
. Besides, the device
exhibits an outstanding cyclic stability of 99.2% after 5000 GCD cycles.
2. Experimental setup
2.1. Materials
Manganese Chloride (MnCl2).4H₂O, Nickel chloride (NiCl2)⋅2H₂O),
and disodium hydrogen phosphate (Na2HPO4), are acquired from the
Sigma. Potassium hydroxide (KOH), activated carbon (AC), N-methyl-2-
2pyrolidone (NMP), polyvanylidene fluoride (PVDF) and acetylene
black, were also bought from Sigma.
2.2. Synthesis of Ni(PO4)2 and Mn(PO4)2 nanoparticles
Ni(PO4)2 nanoparticles were synthesized via sonochemical method
followed via calcination. Firstly 25 ml solution of 0.05 M (NiCl2)⋅2H₂O)
is made in DI water and placed under probe sonicator. Afterward, 25 ml
solution of 5 M Na2HPO4 is dropwise added in above mentioned solution
and sonicated for 45 min. A light greenish colloidal solution is formed.
The power of sonication waves is 950 W and amplitude is kept at 40%.
The synthesized material is collected by centrifugation process and
washed several times with DI water and acetone. The obtained material
is then dried at 60 ◦
C overnight and calcined at 400 ◦
C for 4 h. The Mn
(PO4)2 nanoparticles are synthesized by adopting a similar procedure
and (MnCl2).4H₂O is used as a precursor.
2.3. Synthesis of Ni-Mn(PO4)2 binary composites
The binary composite of Ni-Mn(PO4)2 is made under probe sonicat
ion by doping (MnCl2).4H₂O in (NiCl2)⋅2H₂O) solution. Initially 0.05 M
of (NiCl2)⋅2H₂O) is melted in 15 ml of DI water. After that, 0.0125 M of
(MnCl2).4H₂O is dissolved in 10 ml DI water and dropwise added in the
above solution under constant starring. The mixed solution is then
subjected to prob sonicator and 25 ml solution of 0.75 M Na2HPO4 is
added dropwise in the previous solution under probe sonication. The
sonication is performed for 45 min until the colloidal solution is formed.
The obtained nanoparticles are collected washed and dried overnight as
discussed in the case of (NiCl2)⋅2H₂O). The binary composite is also
calcined at 400 ◦
C for 4 h. The composite is symbolized as NiMn(PO4)2
(see Fig. 1).
3. Results and discussion
3.1. Surface morphology and material composition
The structural morphology and phase purity of the synthesized
nanoparticles are studied by using XRD technique. Fig. 2 demonstrates
the XRD pattern of all the synthesized samples. The obtained pattern
corresponds to Ni(PO4)2 (JCPD, card no. 038–1473) [34,35]. The two
humps appeared between 2θ angle of 21–35 affirms the amorphous
nature of Ni(PO4)2 [29]. Similarly the small diffraction peaks are
observed corresponds to Mn(PO4)2 (JCPD, card no. 03–0426) [36]. The
low intensity of peaks and small humps in the XRD pattern attributes to
the amorphous nature of synthesized materials [29]. The obtained
S. Alam and M.Z. Iqbal
3. Ceramics International 47 (2021) 11220–11230
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diffraction pattern is in well agreement with the report literature of
nickel and manganese phosphate [29,30,36,37]. The surface
morphology of all the synthesized NiMn(PO4)2 based binary nano
composites is studied by employing SEM analysis. Fig. 3 (a) represents
the SEM image of the composites which indicates the formation of NiMn
(PO4)2 nanoflakes. Furthermore, the elemental composition of the
composite is also investigated by performing energy-dispersive X-ray
spectroscopy (EDX). The EDX of the NiMn(PO4)2 nanoflakes is demon
strated in Fig. 3(b–c). The observed peaks of EDX affirm the existence of
Ni, Mn, P, O, Cl, and C elements which reveals the formation of binary
metallic phosphate. There is no impurity peak observed in EDX which
confirms the purity of synthesized material.
3.2. Electrochemical performance
3.2.1. Cyclic voltammetry
The CV measurements are performed to investigate the electro
chemical performance of the synthesized materials in three electrode
assembly. The Pt wire and Hg/HgO are used as counter and reference
electrodes respectively. Measurements are performed in a potential
window range of 0.6 V and 1 M KOH is used as an electrolyte. The CV
curves of all three electrodes at various scan rates are demonstrated in
Fig. 4(a–c). The prominent oxidation and reduction peaks are observed
in the voltammograms indicates the occurrence of redox faradaic re
actions which affirms the battery-grade nature of the tested electrode
materials [49]. It can be noticed that the peak current increases with
increasing scan rates. The oxidation peaks in the CV curve for NiPO4
shifts towards higher potential at higher scan rates due to the unavail
ability of electrolyte ions inside the electrode material. Whereas, the
binary nanocomposites exhibit more prominent redox peaks at high scan
rate reflects its better rate capability and good electrochemical perfor
mance compared to other samples. Fig. 4 (d) represents the CV curves of
all three samples at 3 mVs− 1
. It can be noticed that the CV curve of bi
nary composite demonstrates a higher peak current and maximum area
under the curve. The specific capacity of the tested materials is calcu
lated from the CV curves by using the following expression:
Qs =
1
vm
∫
Vf
Vi
I × V dV (1)
In the above equation, Qs represents specific capacity (Cg− 1
), V de
notes the scan rate (mVs− 1
), m symbolizes the mass of electrode mate
rial, whereas, the integral part of the equation implies the area under the
curve. The binary composite i-e NiMn(PO4)2 exhibits maximum Qs value
of 788 Cg-1
at 3 mVs− 1
and also shown good rate capability compare to
pristine Ni(PO4)2 and Mn(PO4)2. To investigate the different wt % of Mn
in Ni the CV curves for all the samples at 3, 30 and 50 mVs− 1
are per
formed as demonstrated in Fig. 5(a–c). The result reveals that the sample
with 75% Ni and 25% Mn demonstrates maximum area under the curve
and high specific capacity compare to other samples. The trend of Qs
with scan rates is demonstrated in Fig. 5(d). It can be observed that the
Ni0.75Mn0.25(PO4)2 depicts maximum Qs value.
3.2.2. GCD measurements
The charge storage performance of the synthesized nanocomposites
is further investigated by performing GCD measurements in three elec
trode assembly. The measurements are performed in a PW range of
0–0.6 and 1 M KOH is used as an electrolyte. The Pt wire and Hg/Hgo are
used as counter and reference electrode respectively. Fig. 6(a–b) dem
onstrates the discharging curves of all three samples at different current
densities. The non-linearity of discharging curves indicates the battery-
grade nature of synthesized materials as noticed in CV measurements.
The energy storage performance of each electrode is investigated by
calculating the specific capacity by using the following equation [49].
Fig. 1. Schematic illustration of sonochamical synthesis of binary metallic phosphates and washing drying and calcination process.
Fig. 2. XRD pattern of Ni(PO4)2, Mn(PO4)2, and NiMn(PO4)2.
S. Alam and M.Z. Iqbal
4. Ceramics International 47 (2021) 11220–11230
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Qs =
I × Δt
m
(2)
In the above equation, I denotes the total current, Δt represents the
discharging time and m is the mass of the working electrode. From the
above equation it can be perceived that the electrode which possess
maximum discharging time will have high specific capacity. In Fig. 6 (b)
it can be observed that the binary composite of NiMn(PO4)2 exhibit
maximum discharging time compare to other two samples hence, yields
a highest specific capacity of 678 Cg-1
at 0.4 Ag-1
. To ratify the optimum
electrode material the GCD is performed at 1 Ag− 1
for the composite with
50% and 75% Mn doping as demonstrated in Fig. 7 (a). It can be
observed that the Ni75Mn25(PO4)2 indicates best electrochemical per
formance with maximum capacity of 570 Cg-1
at 1 Ag-1
. Fig. 7 (b)
demonstrates the trend of Qs with current densities for all the samples.
The result reveals that 25 wt % Mn in Ni yields best electrochemical
performance.
The trend of Qs for all the samples w.r.t scan rates and current density
is illustrated in Fig. 5(a–b). The maximum Qs value has been measured
for binary composites from both CV and GCD measurements. It can be
observed from Fig. 8(a–b) that the Qs value decreases by increasing the
scan rate and current densities. This is because at lower scan rate and
current value the ions move steadily in the electrolyte and get enough
time to interact with electrode material, also the maximum redox sites
are available and complete redox reaction can be performed which re
sults in maximum Qs at low scan rate and current density values. In
contrast, at the elevated scan rates and current density values the ions
move rapidly and did not get enough time to perform the complete redox
reaction thus results in low Qs value at higher scan rates. The maximum
electrochemical performance of NiMn(PO2)4 can be explained from CV
curves for all the samples. Fig. 3(f) demonstrates the comparison of CV
curves for all the samples at 3 mVs− 1
. The pure Ni(PO2)4 has the
maximum value of redox oxidation state at 0.54V while Mn(PO2)4 has
the maximum oxidation redox peak at 0.46V. The composite comprising
of 25% Mn and 75% of Ni holds a broader redox oxidation peak that
incorporates the maximum redox oxidation potential of both Ni and Mn
whereas, the peak current is almost similar to Ni(PO2)4 which in result
enhances the overall electrochemical performance of composite
compare to all other samples. From the comparison of all three elec
trodes it can be concluded that the binary composite of NiMn(PO4)2
demonstrates maximum Qs value and also possess good rate capability as
seen in Fig. 8(a–b).
3.2.3. Electrochemical impedance spectroscopy (EIS)
To investigate the interaction between electrode and electrolyte and
the mechanism of such interactions the EIS is an important technique. It
provides the information about the internal resistance of electrode ma
terial and the resistance between electrode and electrolyte [50]. Fig. 9
demonstrates the EIS spectrum for all the samples performed in three
electrode assembly in a frequency range of 0.1–105
Hz. The x-axis rep
resents the real part of the impedance and the imaginary part is repre
sented on the y-axis. The zoomed part of EIS is shown in the inset of the
figure for better understanding.
The ESR is measured for all the samples from the point of intersection
with the x-axis. The value of ESR signifies the conductivity of the sam
ple. The estimated ESR values for Ni(PO4)2, NiMn(PO4)2, and Mn(PO4)2
are 1.03, 0.95 and 1.63 Ω respectively. The least value of binary com
posite signifies it highest ionic conductivity compared to the other two
samples. Furthermore, the formation of semicircles with a larger
Fig. 3. Structural morphology and material composition of NiMn(PO4)2 (a) SEM analysis and (b–c) EDX spectrum.
S. Alam and M.Z. Iqbal
5. Ceramics International 47 (2021) 11220–11230
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diameter at high frequency regime signifies charge transfer resistance
(Rct), the sloppy part at lower frequency region represents hydroxyl ions
(OH) diffusion inside the electrode material which indicates the War
burg impedance (W) [51]. The vertical line for NiMn(PO4)2 represents
its low Warburg impedance. The obtained results from EIS measurement
are in good agreement with the CV and GCD measurements which im
plies the best electrochemical performance of NiMn(PO4)2 compare to
pristine phosphates of both the metals.
4. Supercapattery performance measurement
To energy storage performance of the binary composite is further
investigated by fabricating a supercapattery device via utilizing NiMn
(PO4)2 as a positive electrode and AC as a negative electrode. The device
Fig. 4. CV curves of all three samples at different scan rates in three cell assembly. Fig. 2(a–c) Ni(PO4)2, Mn(PO4)2 and NiMn(PO4)2 respectively. (f) Comparison of
the CV profile of all three samples at 3 mVs− 1
.
Fig. 5. CV curves of all the sample with different wt % of Mn in Ni. (a) at 3 mVs− 1
, (b) 30 mVs− 1
and (c) 50 mVs− 1
. (d) Comparison of Qs with scan rate for all
the samples.
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6. Ceramics International 47 (2021) 11220–11230
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Fig. 6. Discharging curves of all the samples at different current densities in three electrode assembly. (a) Ni(PO4)2 (b) Mn(PO4)2 and (c) NiMn(PO4)2. (d) GCD
curves for all three samples at 0.4Ag-1
.
Fig. 7. (a) Discharging curves of all the samples at different wt % of Mn in Ni at 1 Ag-1
. (b) The trend of Qc for all three samples (Ni(PO4)2, 25% Mn, 50% Mn and
75% and Mn(PO4)2) as a function of different current densities.
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7. Ceramics International 47 (2021) 11220–11230
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was tested in two electrode configuration by keeping 1 M KOH as an
electrolyte. Fig. 10 (a) demonstrates the schematic representation of
supercapattery device. The separate CV curve of both the electrodes are
taken at 10 mVs− 1
in three electrode assembly before the fabrication of
the device and is illustrated in Fig. 10 (b). As per literature, for a sig
nificant increase in energy storage performance of supercapacitors, it
should certainly work at larger potential windows. The maximum PW of
the supercapattery device is optimized by performing the CV measure
ments at various PWs as demonstrated in Fig. 10 (c). The maximum PW
is obtained by combining the PW of NiMn(PO4)2 (0–0.7 V) and AC (− 1
to 0 V). Fig. 10 (d) demonstrates the CV measurements of the super
capattery device at different scan rates ranges from 3 to 100 mVs− 1
. The
rectangular behavior of the CV curve in the voltage range of 0–0.5 V
attributes to the EDLC response due to the adsorption of electrolyte ions
at the electrode-electrolyte interface and originate due to capacitive
electrode (AC in this case). Whereas, beyond 0.5 V the redox peaks are
observed originated due to faradaic reaction contribute to the charge
storage mechanism. It can be noticed that the intensity of the redox
peaks increases as the scan rate increases. The combined effect of
capacitive and battery grade electrode can be observed in the CV curves
from the rectangular part and redox peaks respectively. Furthermore,
the CV curves retain its shape even at high scan rate attributes to the
good rate capability of the device.
To evaluate the energy storage parameters of the device GCD mea
surements are performed for the device in two electrode assembly in a
PW of 0–1.7 V by keeping 1 M KOH as an electrolyte. The discharging
curves of the device are demonstrated in Fig. 10 (e). The symmetric
behavior in the GCD curves is due to the capacitive electrode whereas
the slight hump in the curves depicts the presence of redox reactions due
to battery graded electrode. The energy storage capability like specific
energy and specific power of the device is calculated by using the
following relation:
E =
ΔV × Q
3.6 × 2
(3)
P =
E × 3600
Δtdis
(4)
Here, Q represents the specific capacity, Δt denotes the discharging
time, and ΔV represents the PW. The supercapattery reveals a high
specific energy of 64.2 Whkg− 1
, with corresponding specific power, is
340 Wkg-1
at a current density of 0.4 Ag-1
and a maximum value of
specific power is 11896 Wkg-1
at 14 Ag-1
. The comparison of device
performance with previously reported literature in terms of specific
energy and power is demonstrated in Fig. 10 (f) [52–55]. Furthermore,
the detailed comparison of reported work with oxide and phosphate
based electrode materials is provided in Table 1.
Along with excellent specific energy and power the device exhibits,
outstanding life cycle stability demonstrated in Fig. 11 (a). The device
maintains the capacity retention of 99.2% after 5000 continuous GCD
cycles. The slight enhancement in specific capacity after ~300 cycles,
signifies the stabilization of electrode to their maximum limit. As the
number of cycles increases initially the diffusion of electrolyte ions into
the active material increases which in term improves the redox activ
ities. So, this will results in an upsurge in the charge storage capacity of
the device. The ESR value for the device is calculated before and after
the stability measurement by performing EIS in two electrode assembly
and is represented in Fig. 11 (b). The device demonstrates a very low
ERS of 0.34 Ω before stability measurements. The small diameter
semicircle and vertical line in the EIS spectrum at high frequency region
represent the high conductivity of supercapattery device long with
excellent OH−
diffusion into the material respectively, which affirms the
good capacitive behaviors of device. The ESR of the device is increased
slightly from the initial value to 0.65 Ω due to an increase in the internal
resistance of electrode material and electrolyte due to the continue
charge-discharge process. The increase in Warburg resistance is also
observed through a slight shift of vertical line towards low frequency
region which depicts the loss in capacitive behavior of device after 5000
GCD cycles. The overall trend of the EIS spectrum before and after sta
bility measuring shows good cyclic stability of the device.
5. The charge storage mechanism in supercapattery
The analysis of Dunn and his co-workers is utilized at various sweep
rates. The quantitative assessment of capacitive and diffusive contri
butions in the total capacity of the fabricated devices can be calculated
[56].
i(V)=k1v + k2v 1/2
(5)
Fig. 8. The trend of Qc for all three samples as a function of different (a) scan rate, (b) current densities.
Fig. 9. EIS spectrum of all the samples in three cell assembly within a fre
quency range of 0.1–100 KHz. Inset displays the zoom in vision of EIS curves.
S. Alam and M.Z. Iqbal
8. Ceramics International 47 (2021) 11220–11230
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In Eq. (5), the output current for a definite potential is represented by
i(V), v indicates the scan rate and the expressions k1v are capacitive
currents (adsorption of charges results in surface controlled) and k2v1/2
are diffusive currents (diffusion-controlled owing to redox reactions).
Fig. 12(a–f) displayed statistical analysis at different sweep rates for
distinctive separation of currents owing to the surface plus diffusion-
controlled processes.
To the entire capacity of supercapattery, the capacitive contribution
is obtained to be 40% at 3 mVs− 1
scan rate Fig. 12 (a), and diffusive
contribution is found to be dominant at scan rate of 3 mVs− 1
because the
ions get enough time to ample the redox relations at lower scan rates
thus, the charge storage takes place on the aid of battery grade electrode.
An upsurge in the capacitive contribution is observed as the scan rate is
increased and it found to be 78% at 100 mVs− 1
because at high scan rate
the ions didn’t get sufficient time to complete the redox reaction and the
charge storage contribution is dominant for capacitive electrode at
elevated scan rates as seen in bar plot Fig. 12 (b). The above analysis
confirms the hybrid nature of the device as the charge storage contri
bution takes place through both capacitive and battery graded
electrodes.
Furthermore, the power law is applied for the theoretical investiga
tion of the electrochemical performance of the hybrid device. The
following equation demonstrates the power law by defining the relation
between scan rate ‘I’ and current density ‘v’. [57,58].
i = avb
(6)
ln(i) = ln(k) + bln(v) (7)
here, k and b are the adjustable parameters. The exponent of power b is
used to investigate the charge storage mechanism of device. The value of
the b should be equal to 1 for the ideal supercapacitor demonstrates non-
diffusive charge storage whereas, for the batteries, b should be equal to
0.5 depicts the diffusion-controlled charge storage process. Thus, the
value of b lies between 0 and 1 demonstrates the mechanism of charge
storage in supercapattery device [59–61]. Fig. 13 demonstrates the
graph between the log of scan rates for voltages and log of I from 0.8 to
1.35 V. The value of b obtained through linear fitting and lies in the
range of 0.72–0.76 lies exactly in between the range of batteries and SCs.
The range of b values suggested the presence of a both capacitive and
diffusive mechanism for the charge storage process in supercapattery
device. Thus, the results reveal that the fabricated supercapattery device
comprising of binary metal phosphates provides a route towards the
development of efficient and cost-effective energy storage system.
6. Conclusion
We synthesized NiMn(PO4)2 by sono-chemical method; a facile and
cost-effective approach. The surface morphology and elemental analysis
Fig. 10. (a) Schematic illustration of supercapattery device. (b) CV profile of NiMn(PO4)2 and AC at 30 mVs− 1
in three cell assembly. (c) CV measurement of the
device at different PW’s in two cell assembly. (d) CV curves of the supercapattery device at various scan rates in two electrode configuration. (e) Discharging curves
of the fabricated device at various current densities in two cell assembly. (f) Ragone plot represents the comparative study of this work with previously re
ported literature.
Table 1
Comparison of our work with previously reported literature.
S.
no
Electrode
material
Max. Energy density
(Whkg− 1
)
Max. Power density
(Wkg− 1
)
Ref
1. Co3(PO4)2
nanoflakes
43.2 5800 [62]
2. MWCNT-Co3O4-
Ag
16.5 297.5 [63]
3. Sol-gel Co3O4 40 742 [64]
4. CoMoO4 18.89 106 [65]
5. TiO2/RGO 54.3 420.4 [66]
6. Co3(PO4)
2.8H2O
29.2 4687 [67]
7. Ni3(PO4)2-
Ag3PO4
32.4 399.5 [68]
8 Ni-Zn Phosphate 33.7 824.9 [69]
9 NICoP 36 4000 [70]
10 NiCoP 56 5333 [71]
11 Sr3P2/PANI 28.9 5100 [72]
12 This Work 63.8 11,892 This
work
S. Alam and M.Z. Iqbal
9. Ceramics International 47 (2021) 11220–11230
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of the samples were examined through SEM and EDX. The nanoflakes
like morphology was observed. From electrochemical measurements,
the NiMn(PO4)2 demonstrated a high Qs of 678 Cg-1
at 0.4 Ag-1
, which
was used as anode in supercapattery device. Our device exhibited an
outstanding cyclic stability of 99.2% after 5000 GCD cycles, high spe
cific energy of 63.8 Whkg− 1
and a maximum specific power of 11,892
Wkg-1
. The impact of capacitive and diffusive contributions in the total
capacity is studied by employing Dunn’s model. Moreover, the hybrid
nature of device was approved from power law thereby presenting the
trend from 0.723 to 0.785. In conclusion, the contribution of electro
static (capacitive) and Faradaic (diffusive) charge storage mechanism
amplifies the overall energy storage performance of the device.
Declaration of competing interest
The authors declare that they have no known competing financial
interests or personal relationships that could have appeared to influence
the work reported in this paper.
Acknowledgment
This work is supported by Higher Education Commission (HEC) of
Pakistan under the National Research Program for Universities (NRPU)
with Project No. 5544/KPK/NRPU/R&D/HEC/2016.
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Fig. 11. Life cycle stability test of supercapattery device for 5000 GCD cycles. (b) EIS measurements of the device before and after the stability test.
Fig. 12. (a) The pink region depicts the capacitive contribution of at scan rates of 3 mVs− 1
. The light bluish portion is the experimental CV curves at these scan rates
represents diffusive contribution. (b) Bar plot represents the total capacitive and diffusive contribution at different scan rates. (For interpretation of the references to
colour in this figure legend, the reader is referred to the Web version of this article.)
Fig. 13. Log of peak current and scan rates at constant voltages to calculate the
b values of the device.
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