Hydrothermally Assisted Synthesis of Porous Polyaniline@Carbon Nanotubes–Manganese Dioxide Ternary Composite for Potential Application in Supercapattery

In this study, ternary composites of polyaniline (PANI) with manganese dioxide (MnO2) nanorods and carbon nanotubes (CNTs) were prepared by employing a hydrothermal methodology and in-situ oxidative polymerization of aniline. The morphological analysis by scanning electron microscopy showed that the MnO2 possessed nanorod like structures in its pristine form, while in the ternary PANI@CNT/MnO2 composite, coating of PANI over CNT/MnO2, rods/tubes were evidently seen. The structural analysis by X-ray diffraction and X-ray photoelectron spectroscopy showed peaks corresponding to MnO2, PANI and CNT, which suggested efficacy of the synthesis methodology. The electrochemical performance in contrast to individual components revealed the enhanced performance of PANI@CNT/MnO2 composite due to the synergistic/additional effect of PANI, CNT and MnO2 compared to pure MnO2, PANI and PANI@CNT. The PANI@CNT/MnO2 ternary composite exhibited an excellent specific capacity of 143.26 C g−1 at a scan rate of 3 mV s−1. The cyclic stability of the supercapattery (PANI@CNT/MnO2/activated carbon)—consisting of a battery type electrode—demonstrated a gradual increase in specific capacity with continuous charge–discharge over ~1000 cycles and showed a cyclic stability of 119% compared to its initial value after 3500 cycles.


Introduction
Due to the continuous depletion of fossil fuels and the general awareness toward environmental protection and sustainable living, there is an ongoing search for an alternative renewable energy Polymers 2020, 12, 2918 3 of 17 to good contact between the constituents, i.e., PANI, CNT and MnO 2 . The high specific capacity of 131.27 C g −1 along with stability of over 119% cycles holds promise for its application in future enhanced supercapattery devices.

Materials
Aniline and activated carbon (AC) was purchased from Sigma Aldrich. Potassium per manganate (PPs), potassium per sulphate, N-methyl-2-pyrrolidone (NMP), HCl (35%) and ethanol was purchased from Otto chemicals. The CNTs with a diameter of 10-20 nm and length~20 µm were purchased from Hanwha Nanotech, South Korea. The water used in the experiments was deionized water.

Synthesis of MnO 2 , PANI, PANI@CNT and PANI@CNT/MnO 2
MnO 2 nanorods were prepared by hydrothermal methodology. In this protocol, 0.658 g of KMnO 4 was dissolved in 75 mL of water and to which 1.5 mL of HCl was added. The whole system was put under continuous stirring for 15 min and thereafter the solution was charged into Teflon lined hydrothermal reactor of volume 100 mL and kept at 140 • C for 24 h [21]. The final brown color indicated successful formation of MnO 2 . Afterwards centrifugation was used to separate prepared MnO 2 , which was then washed with excess of water and ethanol and subsequently dried at 100 • C for 6 h. PANI@CNT was prepared by in-situ oxidative polymerization of aniline in the presence of CNT. To 100 mL of 0.1 M HCl solution, the CNTs (5 wt% of aniline) were dispersed by stirring and ultrasonic bath. After uniform distribution of CNTs, 1 g of aniline was added to this dispersion for proper adsorption of aniline monomer on CNTs and subsequently the solution of oxidant (1.45 g PPs in 100 mL 1 M HCl) was added to start the polymerization. The reaction mixture turned into greenish black which was filtered after 24 h, washed with water and ethanol and eventually dried at 100 • C for 6 h to get PANI@CNT. Pure PANI was also prepared similarly but without CNTs. For PANI@CNT/MnO 2 , similar methodology as of PANI@CNT was adopted but for the addition of oxidant step. Here a slight modification was done and to the dispersion of aniline and CNTs in 100 mL of 1 M HCl solution, a 100 mL dispersion of 0.2 g of MnO 2 in 1 M HCl was added to affect the polymerization.

Characterization
The morphological and compositional analysis of MnO 2 , PANI, PANI@CNT and PANI@CNT/MnO 2 was conducted by Field emission scanning electron microscopy (FESEM, JSM-7600F (JEOL, Tokyo, Japan)) and energy dispersive X-ray spectroscopy (EDS, Oxford Instruments, High Wycombe, UK). For the crystal structure and phase determination analysis, X-ray diffraction (XRD) was performed in 2θ range of 10 • -90 • (Rigaku, Ultima IV, Tokyo, Japan). Raman analysis was done by Thermo Fisher Scientific instrument (DXR Raman Microscope, Madison, WI, USA). For the elemental analysis and interactions between the constituents, X-ray photoelectron spectroscopy (XPS) (PHI 5000 Versa Probe II, Physical Electronics, Chanhassen, MN, USA) was performed at~10 −10 m bar.

Electrodes Development and Electrochemical Analysis
To develop supercapattery, the prepared composites were used as the positive and AC as the negative electrode. For the fabrication of electrodes, active materials (MnO 2 , PANI, PANI@CNT and PANI@CNT/MnO 2 ) were coated by drop cast method on nickel foam of 1 × 1 cm 2 area. Firstly, a slurry was prepared by mixing the active material (75%), AC (15 wt%), and PVdF (10 wt%) in NMP and was stirred at ambient conditions for 24 h in order to get a homogenous slurry. The slurry was coated on the nickel foam by drop casting and was subsequently heated at 90 • C for 12 h. The active material was loaded on all electrodes in the mass of~5.00 mg.
An electrochemical workstation (Gamry Interface 1000 Instrument, Warminster, PA, USA) was utilized to examine the electrochemical behavior. A potential window of 0-0.5 V was used in cyclic Polymers 2020, 12, 2918 4 of 17 voltammetry (CV) versus Ag/AgCl reference electrode. The current densities of 0.3 to 0.8 A g −1 at 0.5 V were used for galvanostatic-charge-discharge (GCD) studies and electrochemical impedance spectroscopy (EIS) was carried out in the range 0.01-100 kHz at a fixed AC voltage of 10 mV (RMS, root mean square potential amplitude). All electrochemical measurements were performed in 0.1 M KOH aqueous electrolyte.

Morphological Characterizations
The SEM micrographs of MnO 2 , PANI, PANI@CNT and PANI@CNT/MnO 2 are presented in Figure 1. In the case of MnO 2 , highly monodispersed MnO 2 rods with shaped defined edges can be clearly seen (Figure 1a). The diameter of the rods varies from 60-120 nm while its length is in the range of 500-600 nm with many intermediate smaller sized rods also in the vicinity. It can be interpreted that the presence of many smaller particles on MnO 2 or smaller sized rods may be due to the breakage of larger rods or due to the small amount of KMnO 4 which failed to grow into rods [22]. Pure PANI showed fibrous morphology of diameter~30-70 nm with some larger fibers of length exceeding 400 nm while some smaller sized rods are also seen ( Figure 1b). The fibrous morphology of PANI is due to the fast polymerization of aniline during the rapid mixing technique as explained in our previous report [23]. In the case of PANI@CNT, similar morphology as in the case of PANI was observed with little or no observance of CNT owing to the surface coating of PANI over it ( Figure 1c) [24]. The ternary composite PANI@CNT/MnO 2 showed striking different morphology of PANI coated CNT/MnO 2 , with fibers showing interrupted or rough surface which is completely different to that of pure PANI and MnO 2 (Figure 1d). It can be interpreted that the part of MnO 2 which oxidizes aniline to PANI, dissolves or disintegrates during the genesis of PANI tubes leading to the breakage and rough outer surface of PANI. The rough interwoven fibrous and porous structure of PANI@CNT/MnO 2 is expected to provide enhanced surface area and will provide channels for the transport of ions or charge carriers.
The EDS analysis of PANI@CNT/MnO 2 in Figure 2 shows the presence of C which corresponds to the carbon skeleton of PANI and CNT, the N corresponds to the imine group of PANI, while the presence of Mn and O confirms the presence of MnO 2 . The small amount of Cl confirms the acid doping of PANI@CNT/MnO 2 composite.
The elemental mapping of PANI@CNT/MnO 2 also showed the presence of C, N, O, Mn and Cl with homogenous dispersion which suggests the efficacy of the synthesis methodology ( Figure 2).

X-ray Diffraction and Raman Studies
The XRD analysis of MnO 2 , PANI, PANI@CNT and PANI@CNT/MnO 2 is presented in Figure 3a. In the case of MnO 2 , the prominent peaks at 2θ = 12.  [25]. PANI emeraldine salt showed a prominent peak at 2θ = 25.28 • with a slight shoulder at 2θ =~15 and 20 corresponding to the 322, 121 and 113 planes respectively, suggesting that most of the PANI is ordered along these crystal planes [26]. The maximum sharpness of 322 plane peak suggests that most of the arrangement is periodicity perpendicular to the polymer chain [27]. PANI@CNT shows two peaks at 2θ =~25.60 • and 43 • corresponding to the reflections due to the graphitic (0 0 2) and (1 0 0) planes [28]. The peak at 2θ =~25 • of CNT also coincided with the 322 peak of PANI, but in contrast to pure PANI, the XRD peak of PANI@CNT at 2θ =~25 • is much shaper and intense owing to the high crystallinity of CNTs. The ternary composite PANI@CNT/MnO 2 shows all the reflections of PANI, CNT and MnO 2 which suggest successful intercalation of the constituents. However, the peaks are of much reduced intensity which might be due to in-situ oxidation of aniline by MnO 2 as it might result in the disruption of MnO 2 crystals during its dissolution, coating of MnO 2 , PANI or by both over CNT.

X-ray Diffraction and Raman Studies
The XRD analysis of MnO2, PANI, PANI@CNT and PANI@CNT/MnO2 is presented in Figure  3a. In the case of MnO2, the prominent peaks at 2θ = 12.71°, 17.99°, 28.69°, 37.54°, 42.03°, 49.80°, 56.30° and 60.30° corresponds well to the crystal planes of α-MnO2 (JCPDS card PDF file no. 44-0141) [25]. PANI emeraldine salt showed a prominent peak at 2θ = 25.28° with a slight shoulder at 2θ = ~15 and 20 corresponding to the 322, 121 and 113 planes respectively, suggesting that most of the PANI is ordered along these crystal planes [26]. The maximum sharpness of 322 plane peak suggests that most of the arrangement is periodicity perpendicular to the polymer chain [27]. PANI@CNT shows two peaks at 2θ = ~25.60° and 43° corresponding to the reflections due to the graphitic (0 0 2) and (1 0 0) planes [28]. The peak at 2θ = ~25° of CNT also coincided with the 322 peak of PANI, but in contrast to pure PANI, the XRD peak of PANI@CNT at 2θ = ~25° is much shaper and intense owing to the high crystallinity of CNTs. The ternary composite PANI@CNT/MnO2 shows all the reflections of PANI, CNT and MnO2 which suggest successful intercalation of the constituents. However, the peaks are of much reduced intensity which might be due to in-situ oxidation of aniline by MnO2 as it might result in the disruption of MnO2 crystals during its dissolution, coating of MnO2, PANI or by both over CNT.
The Raman spectra of CNT and PANI@CNT/MnO2 is presented in Figure 3b. Pure CNT shows a typical G band (derived from the graphite like mode) at 1580 cm -1 . The defects or disorder induced D-band gap is situated at 1346 cm -1 [29]. After coating with PANI and MnO2 in PANI@CNT/MnO2, the spectra of PANI is dominant which confirms good coating of CNT with PANI [30].

X-ray Photoelectron Spectroscopy Studies
The XPS analysis was done to study the composition and chemical states of PANI@CNT/MnO2 ( Figure 4). The survey scan of PANI@CNT/MnO2 (Figure 4a) shows the presence of five major sets of peaks corresponding to C, N, O, Cl and Mn without the observance of any other impurities. The C1s peak corresponds to the residual carbon of the sample and carbon from the XPS instrument. The C1s peak ( Figure 4b) can be deconvoluted into three peaks at 284.71, 285.85 and 288.92 eV corresponding to the aliphatic carbon C-C/C-H, C-O-C and O-C=O [31]. The C-O-C and O-C=O also represents some additional functionality of PANI and CNT which might acts as sites for interaction with each other or MnO2.
The N1s peak ( Figure 4d) can be deconvoluted into three peaks at 399.45, 400.64 and 401.76 eV corresponding to the pyridinic nitrogen, pyrrolic nitrogen/pyridone nitrogen in association with oxygen functionality and quaternary nitrogen respectively [32]. In Mn2p spectra (Figure 4e) two peaks at ~638 and 649 eV with a separation gap of ~11 eV can be attributed to the Mn2p3/2 and Mn2p1/2 respectively. These values are in agreement with the previous reports and indicate +4 oxidation state of Mn [33]. This also suggests successful synthesis of MnO2 and also its state has not changed in the ternary composite. In the O1s spectra ( Figure 4e) the 530.99 eV can be associated with The Raman spectra of CNT and PANI@CNT/MnO 2 is presented in Figure 3b. Pure CNT shows a typical G band (derived from the graphite like mode) at 1580 cm −1 . The defects or disorder induced D-band gap is situated at 1346 cm −1 [29]. After coating with PANI and MnO 2 in PANI@CNT/MnO 2 , the spectra of PANI is dominant which confirms good coating of CNT with PANI [30].

X-ray Photoelectron Spectroscopy Studies
The XPS analysis was done to study the composition and chemical states of PANI@CNT/MnO 2 (

Three Electrodes Electrochemical Studies of MnO2, PANI, PANI@CNT and PANI@CNT/MnO2
Electrochemical studies of the as synthesized ternary composite and its variants were carried out in an alkaline medium (0.1 M KOH) in the potential range of 0 to 0.5 V using Ag/AgCl as reference and platinum wire as counter electrode through cyclic voltammetry (CV), galvanostatic chargedischarge (GCD) at various current densities (0.3-0.8 A g −1 ) and electrochemical impedance spectroscopy (EIS) in a standard three electrodes cell system. Figure 5 shows the electrochemical signature of MnO2, PANI, PANI@CNT and PANI@CNT/MnO2 at different scan rates from 3 to 50 mV s −1 . The lowest and the highest scan rates demonstrate the stability and rate capability of the electrode materials [35]. In each case the redox peaks in the voltammograms can be observed, demonstrating the occurrence of faradic reaction at the electrode which is the property of a battery grade material [36]. Figure 5a shows the MnO2 CV curves at different scan rates. There is a linear increase in the current densities when the scan rates were increased showing the good electrochemical behavior and reached to the maximum current density of 19.88 mA g −1 at a scan rate of 50 mV s −1 as a standalone electrode material when the particles size is in the nano regime [37]. The metal oxides in their pristine forms tend to aggregate, which reduced the electrochemical active sites of the nanomaterials and ultimately affected the electrochemical activity of the electrode materials. In the case of PANI ( Figure  5b), when scanned from 3 to 50 mV s −1 , a maximum current density of 74.76 mA g −1 was observed because PANI is well known conducting polymer and its fibrous morphology is most conductive in nature compared to nanospheres and nanorods [38]. Figure 5c represents CV curves of PANI@CNT. Carbon nanotubes have excellent conductivity and thermal stability. Therefore, due to the additional effect the current density of PANI@CNT was increased to 126.37 mA g −1 at 50 mV s −1 compared to pure PANI. However, the maximum current density (154.84 mA g −1 @ 50 mV s −1 ) was achieved in the case of the ternary composite, PANI@CNT/MnO2 as demonstrated in Figure 5d, which could be due to the synergistic effect of CNT and MnO2 nanoparticles in the ternary composite [39]. Additionally, the porous nature of the ternary composite plays a pivotal role in the perforation of counter ions that help to enhance the conductivity of the active material. When the MnO2 nanorods are embedded in the polymer matrix the phenomena of de-aggregation occurred, which helped to expose the more electroactive site of the MnO2 nanoparticles. Due to the de-aggregation of MnO2 nanoparticles and addition of CNT in polymer matrix, the highest conductivity was achieved due to the synergistic The N1s peak (Figure 4d) can be deconvoluted into three peaks at 399.45, 400.64 and 401.76 eV corresponding to the pyridinic nitrogen, pyrrolic nitrogen/pyridone nitrogen in association with oxygen functionality and quaternary nitrogen respectively [32]. In Mn2p spectra (Figure 4e) two peaks at~638 and 649 eV with a separation gap of~11 eV can be attributed to the Mn2p3/2 and Mn2p1/2 respectively. These values are in agreement with the previous reports and indicate +4 oxidation state of Mn [33]. This also suggests successful synthesis of MnO 2 and also its state has not changed in the ternary composite. In the O1s spectra ( Figure 4e) the 530.99 eV can be associated with the oxygen attached to Mn. The other bands at 532.77 and 534.69 eV is due to organic C=O or H-O-H and C=O, respectively [34]. The small amount of Cl in the survey scan is from HCl due to the acid doping of PANI.

Three Electrodes Electrochemical Studies of MnO 2 , PANI, PANI@CNT and PANI@CNT/MnO 2
Electrochemical studies of the as synthesized ternary composite and its variants were carried out in an alkaline medium (0.1 M KOH) in the potential range of 0 to 0.5 V using Ag/AgCl as reference and platinum wire as counter electrode through cyclic voltammetry (CV), galvanostatic charge-discharge (GCD) at various current densities (0.3-0.8 A g −1 ) and electrochemical impedance spectroscopy (EIS) in a standard three electrodes cell system. Figure 5 shows the electrochemical signature of MnO 2 , PANI, PANI@CNT and PANI@CNT/MnO 2 at different scan rates from 3 to 50 mV s −1 . The lowest and the highest scan rates demonstrate the stability and rate capability of the electrode materials [35]. In each case the redox peaks in the voltammograms can be observed, demonstrating the occurrence of faradic reaction at the electrode which is the property of a battery grade material [36]. Figure 5a shows the MnO 2 CV curves at different scan rates. There is a linear increase in the current densities when the scan rates were increased showing the good electrochemical behavior and reached to the maximum current density of 19.88 mA g −1 at a scan rate of 50 mV s −1 as a standalone electrode material when the particles size is in the nano regime [37]. The metal oxides in their pristine forms tend to aggregate, which reduced the electrochemical active sites of the nanomaterials and ultimately affected the electrochemical activity of the electrode materials. In the case of PANI (Figure 5b), when scanned from 3 to 50 mV s −1 , a maximum current density of 74.76 mA g −1 was observed because PANI is well known conducting polymer and its fibrous morphology is most conductive in nature compared to nanospheres and nanorods [38]. Figure 5c represents CV curves of PANI@CNT. Carbon nanotubes have excellent conductivity and thermal stability. Therefore, due to the additional effect the current density of PANI@CNT was increased to 126.37 mA g −1 at 50 mV s −1 compared to pure PANI. However, the maximum current density (154.84 mA g −1 @ 50 mV s −1 ) was achieved in the case of the ternary composite, PANI@CNT/MnO 2 as demonstrated in Figure 5d, which could be due to the synergistic effect of CNT and MnO 2 nanoparticles in the ternary composite [39]. Additionally, the porous nature of the ternary composite plays a pivotal role in the perforation of counter ions that help to enhance the conductivity of the active material. When the MnO 2 nanorods are embedded in the polymer matrix the phenomena of de-aggregation occurred, which helped to expose the more electroactive site of the MnO 2 nanoparticles. Due to the de-aggregation of MnO 2 nanoparticles and addition of CNT in polymer matrix, the highest conductivity was achieved due to the synergistic effect of the contributing components in ternary composite as shown in comparison plot (Figure 5d). In all cases, there is a slight peak potential shift at high scan rates due to the asynchronous movement of the counter ions. These results are providing the evidence of useful strategy that a combination of three components (PANI, CNT, MnO 2 ) in the form of composite by a facile synthesis protocol and porosity can produce enhanced electrochemical signature than the individuals. A comparison plot (Figure 5e) of all variants shows the systematic increase in the current densities. The specific capacity (Q S ) for all electrode materials from CV curves was calculated using the following Equation (1) [40]: where Q S , m, υ, and integral part of the equation represent specific capacity (C g −1 ), active mass (g), scan rate (mV s −1 ) and area under the I-V curve respectively. The Q S values calculated at 3 mV s −1 for MnO 2 , PANI, PANI@CNT, and PANI@CNT/MnO 2 are 34.71, 86.02, 118.47, and 143.26 C g −1 , respectively. The specific capacity versus scan rates is plotted in Figure 5f. It could be concluded that specific capacity depleted at higher scan rate, but the ternary composite is the best sustaining electrode material even at high scan rate among other samples when tested under the same conditions. The GCD studies presented in Figure 6 were conducted at a fix potential of 0.5 V vs. Ag/AgCl at different current densities. It is obvious from the GCD curves (Figure 6a-d) that there is a systematic increase in the discharge time for all four variants, but the ternary composite takes a lead among all, as shown in the comparison plot (Figure 6e). The non-triangular GCD curves vouch the non-electrostatic behavior of the electrode materials. Similarly, Q S values were also calculated from GCD curves for all variants using the following Equation (2) [41]: where I, ∆t and m represent current density, discharge time and active mass in the equation, respectively. The obtained Q S values at current density 0.3 A g −1 are 32.98, 95.04, 128.73, and 153.82 C g −1 for MnO 2 , PANI, PANI@CNT, and PANI@CNT/MnO 2 , respectively. The specific capacity values at various current densities are plotted in Figure 6f. It is clear the ternary composite showed the highest specific capacity and better rate capability among all other variants. The GCD studies presented in Figure 6 were conducted at a fix potential of 0.5 V vs. Ag/AgCl at different current densities. It is obvious from the GCD curves (Figure 6a-d) that there is a systematic increase in the discharge time for all four variants, but the ternary composite takes a lead among all, as shown in the comparison plot (Figure 6e). The non-triangular GCD curves vouch the nonelectrostatic behavior of the electrode materials. Similarly, values were also calculated from GCD curves for all variants using the following Equation (2)   where I, ∆t and m represent current density, discharge time and active mass in the equation, respectively. The obtained values at current density 0.3 A g −1 are 32.98, 95.04, 128.73, and 153.82 C g −1 for MnO2, PANI, PANI@CNT, and PANI@CNT/MnO2, respectively. The specific capacity values at various current densities are plotted in Figure 6f. It is clear the ternary composite showed the highest specific capacity and better rate capability among all other variants.  48 Ω, respectively. The best performing electrode material was then selected for device fabrication. In this case, it is concluded from all above electrochemical studies that ternary composite, PANI@CNT/MnO 2 is the best battery type electrode material which can be utilized for hybrid device assembly.
at an alternating voltage of 10 mV (RMS) in the frequency range of 0.01-100 kHz. The Nyquist plot for different variants are shown in Figure 7. The graph demonstrates that the ternary composite (0.49 Ω) has the least charge transfer resistance compared to PANI (1.40 Ω), MnO2 (0.54 Ω) and PAN@CNT (0.62 Ω) as well as most vertical line parallel to the imaginary axis (-Z'') showing the best charge storage capacity. Similarly, ESR values obtained for MnO2, PANI, PANI@CNT, and PANI@CNT/MnO2 are 0.45, 0.22, 0.38, and 0.48 Ω, respectively. The best performing electrode material was then selected for device fabrication. In this case, it is concluded from all above electrochemical studies that ternary composite, PANI@CNT/MnO2 is the best battery type electrode material which can be utilized for hybrid device assembly.  Figure 7 shows the electrochemical impedance spectroscopy (EIS) spectrum in high frequency region.

Fabrication and Characterization of Two Electrodes Assembly (PANI@CNT/MnO2//AC)
The two electrodes assembly was developed using a nickel foam coated ternary composite, PANI@CNT/MnO2 as positive electrode (battery-grade material) and activated carbon (AC) coated as negative electrode (capacitive material). Both electrodes were coupled together by placing porous membrane in between them. In this assembly two different electrodes were used, i.e., supercapacitor electrodes and battery type electrodes, known as supercapattery, which can store charge electrostatically and electrochemically. Before combining them together both were tested individually in three electrodes cell to know their working potential window and electrochemical signature. Figure 8a shows that the AC is capacitive electrode with a potential window of −1 to 0 V whereas ternary composite is pseudocapacitive with potential window, 0 to 0.5 V. Figure 8b shows the graphical demonstration of the assembled device in which positive potential is applied to battery type electrode whereas negative potential to capacitive electrode. The electrochemical studies (CV, GCD and stability) of two electrodes assembly were conducted in 0.1 M KOH in the potential range of 0 to 1.5 V.  Figure 7 shows the electrochemical impedance spectroscopy (EIS) spectrum in high frequency region.

Fabrication and Characterization of Two Electrodes Assembly (PANI@CNT/MnO 2 //AC)
The two electrodes assembly was developed using a nickel foam coated ternary composite, PANI@CNT/MnO 2 as positive electrode (battery-grade material) and activated carbon (AC) coated as negative electrode (capacitive material). Both electrodes were coupled together by placing porous membrane in between them. In this assembly two different electrodes were used, i.e., supercapacitor electrodes and battery type electrodes, known as supercapattery, which can store charge electrostatically and electrochemically. Before combining them together both were tested individually in three electrodes cell to know their working potential window and electrochemical signature. Figure 8a shows that the AC is capacitive electrode with a potential window of −1 to 0 V whereas ternary composite is pseudocapacitive with potential window, 0 to 0.5 V. Figure 8b shows the graphical demonstration of the assembled device in which positive potential is applied to battery type electrode whereas negative potential to capacitive electrode. The electrochemical studies (CV, GCD and stability) of two electrodes assembly were conducted in 0.1 M KOH in the potential range of 0 to 1.5 V.
The CV studies were conducted at different potential windows (0-0.5, 0-0.75, 0-1.0, 0-1.25 and 0-1.5 V) to verify the maximum working potential range as shown in Figure 8c. The assembled hybrid device then scanned at various rates from 3 to 100 mV s −1 at a fix potential window of 0 to 1.5 V as demonstrated in Figure 8d to analyze the rate capability. The shape of the CVs was well conserved even at higher scan rates thereby representing the marvelous rate capability. The shape of the CVs is neither rectangular nor humpy, showing the contribution of both energy storage mechanism, i.e., non-faradaic (capacitive) and faradaic (diffusive). In GCD studies (Figure 9a), similar trend was observed because the curves were not completely rectangular but each one has little shoulder. Here again, the assembled hybrid device demonstrating the charge storage mechanism is contributed by both capacitive and diffusive processes. The Q S values were calculated form the GCD curves for the assembled hybrid device at various current densities using Equation (2). The CV studies were conducted at different potential windows (0-0.5, 0-0.75, 0-1.0, 0-1.25 and 0-1.5 V) to verify the maximum working potential range as shown in Figure 8c. The assembled hybrid device then scanned at various rates from 3 to 100 mV s −1 at a fix potential window of 0 to 1.5 V as demonstrated in Figure 8d to analyze the rate capability. The shape of the CVs was well conserved even at higher scan rates thereby representing the marvelous rate capability. The shape of the CVs is neither rectangular nor humpy, showing the contribution of both energy storage mechanism, i.e., non-faradaic (capacitive) and faradaic (diffusive). In GCD studies (Figure 9a), similar trend was observed because the curves were not completely rectangular but each one has little shoulder. Here again, the assembled hybrid device demonstrating the charge storage mechanism is contributed by both capacitive and diffusive processes. The values were calculated form the GCD curves for the assembled hybrid device at various current densities using Equation (2).
The highest specific capacity of 131.27 C g −1 was found at current density of 0.4 A g −1 for the assembled hybrid device as shown in Figure 9a.
The energy density (E) and power density (P) are the major parameters to assess the working of an energy storage device which were calculated using the following Equations (3) and (4): where , ∆V, and ∆t represent the specific capacity (C g −1 ), potential window (V) and discharge time (s) of the hybrid device, respectively. The obtained values of energy density and power density are The highest specific capacity of 131.27 C g −1 was found at current density of 0.4 A g −1 for the assembled hybrid device as shown in Figure 9a.
The energy density (E) and power density (P) are the major parameters to assess the working of an energy storage device which were calculated using the following Equations (3) and (4): where Q S , ∆V, and ∆t represent the specific capacity (C g −1 ), potential window (V) and discharge time (s) of the hybrid device, respectively. The obtained values of energy density and power density are plotted in Figure 9c. The maximum energy density (27.17 Wh kg −1 ) was obtained at a current density of 0.3 A g −1 with the corresponding power density of 298.00 W kg −1 . An inverse relation was noticed between energy density and power density. When the power density was stepped up from 298.00 to 1995.00 W kg −1 , energy density depleted down from 20.47 to 15.07 W kg −1 . These results proved the excellent working of the hybrid assembled device using the novel ternary composite when assessed based on energy density, power density and specific capacity. Another important parameter for energy storage devices is the stability test. The assembled hybrid device was subjected to charge-discharge cycles for over 3500 cycles. Figure 9d shows the initial increase in the specific capacity which is due to the activation of polymer composite. A similar trend has been reported in many other articles, especially, where conducting polymers were used in the composites [3,42]. However, after about 1000 cycles the stability in the specific capacity was observed, and finally at the end of 3500 cycles, excellent (119.00%) specific capacity with coulombic efficiency of 93.50% was demonstrated by the assembled hybrid device. These results advocate the successful synthesis of porous ternary composite in which three components were combined by a simple hydrothermal method coupled with in-situ oxidative polymerization to achieve synergistic/additional electrochemical effect and subsequently utilized as a battery type electrode material in supercapattery. We compared our results with the reported literature on polyaniline based composite electrode materials, which is presented in Table 1. energy storage devices is the stability test. The assembled hybrid device was subjected to chargedischarge cycles for over 3500 cycles. Figure 9d shows the initial increase in the specific capacity which is due to the activation of polymer composite. A similar trend has been reported in many other articles, especially, where conducting polymers were used in the composites [3,42]. However, after about ~1000 cycles the stability in the specific capacity was observed, and finally at the end of 3500 cycles, excellent (119.00%) specific capacity with coulombic efficiency of 93.50% was demonstrated by the assembled hybrid device. These results advocate the successful synthesis of porous ternary composite in which three components were combined by a simple hydrothermal method coupled with in-situ oxidative polymerization to achieve synergistic/additional electrochemical effect and subsequently utilized as a battery type electrode material in supercapattery. We compared our results with the reported literature on polyaniline based composite electrode materials, which is presented in Table 1.

Conclusions
In summary, PANI@CNT/MnO 2 nanocomposites was prepared by the combination of in-situ oxidative polymerization and hydrothermal reaction. The FESEM images showed fibers with interrupted or rough surfaces, which is expected to provide an enhanced surface area and facilitate in the transport of ions or charge carriers. The XRD and XPS analyses of PANI@CNT/MnO 2 showed peaks corresponding to the MnO 2 , CNT, and PANI, thereby suggesting the efficacy of the synthesis methodology. The electrochemical studies were carried out to analyze the voltammetric character through a typical three electrode system and applied voltages ranging from 0 to 0.5 V. PANI@CNT/MnO 2 battery type ternary nanocomposite showed highest current density of 154.84 mA g −1 @ 50 mV s −1 and specific capacity of 143.26 F g −1 at 3 mV s −1 in comparison to 34.71 for MnO 2 , 86.02 for PANI and 118.47 C g −1 for PANI@CNT. The galvanostatic charge-discharge studies showed that there is systematic increase in the discharge time for all four variants but PANI@CNT/MnO 2 ternary composite demonstrated the best electrochemical performance in terms of longer discharge duration. The specific capacity from GCD curves at current density 0.3 A g −1 were 32.98, 95.04, 128.73, and 153.82 C g −1 for MnO 2 , PANI, PANI@CNT, and PANI@CNT/MnO 2 , respectively. The Nyquist plots for the performed EIS study showed that PANI@CNT/MnO 2 has the smallest radius among all other electrode materials at high frequencies with a more vertical line at low frequencies parallel to the imaginary axis. This confirms that PANI@CNT/MnO 2 battery type material possesses highest capacity of charge storage and least resistance against the charge transfer. The enhanced performance of PANI@CNT/MnO 2 can be attributed to the high thermal and electrical conductivity of the constituents which assist in smooth conductive path for the transportation of charge carriers along MnO 2 , CNT and PANI. Apart from this, the assembled supercapattery-consisting of the battery type ternary composite as a positive and an activated carbon as the negative electrode-delivered the highest specific capacity of 131.27 C g −1 which was found at a current density of 0.4 A g −1 . The maximum energy density of 27.17 Wh kg −1 was obtained at a current density of 0.3 A g −1 with the corresponding power density of 298.00 W kg −1 . The cyclic stability of the fabricated device showed that the PANI@CNT/MnO 2 battery type ternary composite retained 119% capacitance even after 3500 cycles. The high specific capacitance combined with excellent cyclic stability projects PANI@CNT/MnO 2 to be a promising battery type material for high performance supercapattery.