Hierarchical Manganese–Iron-Layered Double Hydroxide Nanosheets for Asymmetric Supercapacitors

: This work presents a synthesis of hierarchical manganese–iron-layered double hydroxide (MnFe-LDH) nanostructured electrodes using the hydrothermal synthesis route by varying the reaction time for electrochemical energy storage applications. The electrochemical behavior of the MnFe-LDH electrodes synthesized at di ﬀ erent reaction times was analyzed in a three-electrode cell conﬁguration using 2 M KOH electrolyte. The uniform and well-organized MnFe-LDH nanosheet electrode (MnFe-12h) showed the maximum areal capacitance of 2013 mFcm − 2 at a 5 mVs − 1 scan rate, and 1886 mFcm − 2 at a 25 mA applied current. Furthermore, the electrochemical behavior of MnFe-12h was examined by assembling an asymmetric cell device using activated carbon (AC) as a negative electrode and MnFe-12h as a positive electrode and it was tested in a wide voltage window range of 0.0 to 1.6 V. This asymmetric cell device achieved an appropriate energy density of 44.9 µ W h cm − 2 (55.01 W h kg − 1 ), with a power density of 16 mW cm − 2 (5000 W kg − 1 ) at an applied current of 10 mA, and had a long-term cycling stability (93% capacitance retention after 5000 cycles) within the 1.6 V operating voltage window.


Introduction
The current global situation due to climate change demands green energy alternatives such as renewable energies in order to preserve our ecosystem. It is highly essential to store these renewable energies to be able to use them on demand. Supercapacitors (SCs), also known as ultracapacitors owing to their high capacitance, are the most appealing energy storage systems. The fast charge-discharge rate, good cycling stability, high power density, low cost, and eco-friendliness of SCs is the reason why people are turning their attention to them [1][2][3]. The charge storage mechanisms in SCs classify them as electric double-layer capacitors (EDLCs) and pseudocapacitors. In EDLCs, the adsorption/desorption of electrolytic ions takes place in the space charge double-layer region of the material, leading to limited energy density. In pseudocapacitors, the energy can be stored to a greater degree due to the faradaic charge transfer process [4,5].
Layered double hydroxides (LDHs) have attracted much attention as an electrode material for supercapacitors owing to their high surface area, high redox activity, highly interconnected morphology, low cost, and environmental benignness [6,7]. The hydroxide layers in the LDH structure contain positive charges and anions among the layers. LDHs possess flexible anionic exchange and a laminar structure that helps electron and ion transport during the charging/discharging process in SCs [8]. Additionally, the hydrophilicity in LDHs is highly favorable for the diffusion of ions in aqueous electrolyte.

Characterization of Electrodes
X-ray diffraction (XRD; Panalytical, Malvern, UK) was performed using Cu Kα radiation. X-ray photoelectron spectroscopy (XPS; K-alpha, Thermo Scientific, Loughborough, UK) was used to govern the surface chemical composition. The surface features of the film were analyzed by fieldemission scanning electron microscopy (FESEM; S-4800 HITACHI, Ltd., Tokyo, Japan). Electrochemical measurements, including cyclic voltammetry (CV), electrochemical impedance spectroscopy (EIS), and galvanostatic charge/discharge (GCD) measurements, were performed in 2 M KOH electrolyte in a conventional three-electrode arrangement consisting of synthesized MnFe-LDH as a working electrode, graphite as a counter electrode, and saturated calomel as a reference electrode (SCE) using a ZIVE SP5 electrochemical workstation (WonAtech, Seoul, Korea). For each electrode, the area of the deposited MnFe-LDH was constant (1 cm × 1 cm). For the two electrode measurements, an asymmetric cell device was fabricated using MnFe-12h as a positive electrode and activated carbon (AC) as a negative electrode. The AC electrode was prepared as mentioned in our previous report [18]. Briefly, to prepare the AC electrode, the activated carbon, binder poly (tetrafluoroethylene), and carbon black in a weight ratio of 80:10:10 were mixed together. The obtained mixture was coated onto the Ni foam and then air-dried at 75 °C for 12 h. The device was assembled by inserting filter paper soaked in 2 M KOH between the positive (MnFe-12h) and negative (AC) electrodes and sealed using Parafilm. The detailed schematic representation of the asymmetric device fabrication is as shown in Figure 1b.

Results and Discussion
The schematic illustration of the formation of different nanostructures of MnFe-LDH using the hydrothermal route with varying reaction times is depicted in Figure 1a. The hydrothermal reaction mainly comprises the hydrolysis of urea (CO(NH 2 ) 2 , which produces OH − ions. These released OH − ions interact with the dissociated Mn 2+ and Fe 2+ ions from KMnO 4 and FeSO 4 , respectively, forming MnFehydroxide [11,17]. The probable chemical reactions happening during the formation of MnFe-hydroxide through hydrothermal treatment can be signified by the following reactions:

FESEM
The surface morphological features of the MnFe-LDH electrode were studied by FESEM. Figure 2a-l shows FESEM images of the MnFe-9h, MnFe-12h and MnFe-24h samples. In the FESEM images at lower magnification (Figure 2a,e,i), it is clearly seen that the Ni foam's surface is fully covered by the synthesized MnFe-LDH material, for all synthesized electrodes grown at 9, 12, and 24 h, respectively. Initially, after a 9 h hydrothermal reaction, an aggregation of nanoparticles of the MnFe-LDH structure appears, as shown in Figure 2a-d, and a partial growth of the nanosheet is also observed. As the reaction time goes on, increasing to 12 h, the nanoparticle aggregates are turned into a network of interconnected nanosheets (Figure 2e-h). These MnFe-LDH nanosheets appear in a bunch resembling petals of a flower. It should be noted that the large number of even and dense MnFe-LDH nanosheets is seen firmly anchored on the whole surface of the Ni foam. The nanosheets are very thin, with an average thickness of~15-20 nm. The thin and interconnected nanosheets are highly beneficial for ionic transport, mainly due to their enhanced reactive surface area. Similarly, the layered structure of LDHs offers an easy access to electrolyte ions to diffuse through the entire nanosheet, which is useful for a highly efficient utilization of active sites [23]. Finally, for the 24 h hydrothermal reaction time, the formation of large leaf-like nanostructures with voids in between these nanostructures is observed (Figure 2i-l); this may be due to the higher reaction time.

XRD
The crystal structure and phase of a MnFe-LDH nanostructure are determined by an X-ray diffraction study; Figure 4a presents the XRD patterns of the MnFe-LDH structure of the MnFe-9h, MnFe-12h, and MnFe-24h samples. The XRD patterns show a series of (00l) reflections characteristic of layered structures, affirming the LDH structure of MnFe-LDH. The peaks correspond to the (003), (006), and (009) planes of the MnFe-LDH structure, which again confirms the formation of the MnFe-layered structure. The nature of XRD peaks is broad, indicating a nanocrystallinity of the MnFe-LDH structure. Similar peaks were obtained for MnFe-LDH elsewhere [20,24]. Apart from the peaks due to MnFe-LDH, there are sharp peaks at 44 • , 52 • , and 76 • , which are assigned to the Ni foam substrate, denoted by "∆". In addition, some peaks are detected, ascribed to the precursors used for the preparation of the electrodes [18].

XRD
The crystal structure and phase of a MnFe-LDH nanostructure are determined by an X-ray diffraction study; Figure 4a presents the XRD patterns of the MnFe-LDH structure of the MnFe-9h, MnFe-12h, and MnFe-24h samples. The XRD patterns show a series of (00l) reflections characteristic of layered structures, affirming the LDH structure of MnFe-LDH. The peaks correspond to the (003), (006), and (009) planes of the MnFe-LDH structure, which again confirms the formation of the MnFelayered structure. The nature of XRD peaks is broad, indicating a nanocrystallinity of the MnFe-LDH structure. Similar peaks were obtained for MnFe-LDH elsewhere [20,24]. Apart from the peaks due

XRD
The crystal structure and phase of a MnFe-LDH nanostructure are determined by an X-ray diffraction study; Figure 4a presents the XRD patterns of the MnFe-LDH structure of the MnFe-9h, MnFe-12h, and MnFe-24h samples. The XRD patterns show a series of (00l) reflections characteristic of layered structures, affirming the LDH structure of MnFe-LDH. The peaks correspond to the (003), (006), and (009) planes of the MnFe-LDH structure, which again confirms the formation of the MnFelayered structure. The nature of XRD peaks is broad, indicating a nanocrystallinity of the MnFe-LDH structure. Similar peaks were obtained for MnFe-LDH elsewhere [20,24]. Apart from the peaks due  to MnFe-LDH, there are sharp peaks at 44°, 52°, and 76°, which are assigned to the Ni foam substrate, denoted by "∆". In addition, some peaks are detected, ascribed to the precursors used for the preparation of the electrodes [18].

XPS
The XPS of MnFe-LDH mainly involve Mn, Fe, and O components, as depicted in Figure

Electrochemical Study
The electrochemical behavior of the MnFe-LDH nanostructured electrodes grown at different hydrothermal reaction times was studied by measuring the CV and GCD curves using a conventional three-electrode system. The CV curves of MnFe-9h, MnFe-12h, and MnFe-24h recorded in the potential window of −0.1 to +0.5 versus SCE at 5 mVs −1 are as shown in Figure 5a. The pair of redox peaks observed for all three electrodes (MnFe-9h, MnFe-12h, and MnFe-24h) suggests the faradaic charge storage behavior of MnFe-LDH. It was observed that the area under the curve and, hence, the current from the CV curve varied with respect to the hydrothermal reaction time, as a clear

Electrochemical Study
The electrochemical behavior of the MnFe-LDH nanostructured electrodes grown at different hydrothermal reaction times was studied by measuring the CV and GCD curves using a conventional three-electrode system. The CV curves of MnFe-9h, MnFe-12h, and MnFe-24h recorded in the potential window of −0.1 to +0.5 versus SCE at 5 mVs −1 are as shown in Figure 5a. The pair of redox peaks observed for all three electrodes (MnFe-9h, MnFe-12h, and MnFe-24h) suggests the faradaic charge storage behavior of MnFe-LDH. It was observed that the area under the curve and, hence, the current from the CV curve varied with respect to the hydrothermal reaction time, as a clear modification is seen from the FESEM images ( Figure 2). With the increase in hydrothermal reaction time from 9 h to 12 h, the area under the CV curve increases and the surface morphology changes from nanoparticles with Energies 2020, 13, 4616 7 of 14 few nanosheets to the uniform and well-organized nanosheets, providing more accessible reaction sites to the electrolyte ions. After further increasing the hydrothermal reaction time from 12 h to 24 h, the observed decrease in the CV current may be due to the formation of large leaf-like nanostructures covering the active materials, which then resulted in difficult access for the electrolyte ions. According to the previous literature, the shape of the CV curves obtained for MnFe-LDH electrodes defines the battery-type behavior of the synthesized electrodes; it is thus necessary to also discuss the areal capacitance in terms of areal capacities [26][27][28]. The areal capacitance values (capacities) calculated from the CV curves at 5 mVs −1 for MnFe-9h, MnFe-12h, and MnFe-24h were 1196 mFcm −2 (717 mCcm −2 ), 2013 mFcm −2 (1208 mCcm −2 ), and 1802 mFcm −2 (1081 mCcm −2 ), respectively.
Energies 2020, 13, x FOR PEER REVIEW 7 of 15 modification is seen from the FESEM images ( Figure 2). With the increase in hydrothermal reaction time from 9 h to 12 h, the area under the CV curve increases and the surface morphology changes from nanoparticles with few nanosheets to the uniform and well-organized nanosheets, providing more accessible reaction sites to the electrolyte ions. After further increasing the hydrothermal reaction time from 12 h to 24 h, the observed decrease in the CV current may be due to the formation of large leaf-like nanostructures covering the active materials, which then resulted in difficult access for the electrolyte ions. According to the previous literature, the shape of the CV curves obtained for MnFe-LDH electrodes defines the battery-type behavior of the synthesized electrodes; it is thus necessary to also discuss the areal capacitance in terms of areal capacities [26][27][28]. The areal capacitance values (capacities) calculated from the CV curves at 5 mVs −1 for MnFe-9h, MnFe-12h, and MnFe-24h were 1196 mFcm −2 (717 mCcm −2 ), 2013 mFcm −2 (1208 mCcm −2 ), and 1802 mFcm −2 (1081 mCcm −2 ), respectively. The CV curves of the MnFe-9h, MnFe-12h, and MnFe-24h electrodes recorded with varying scan rates from 5 to 100 mVs −1 , in a potential window of −0.1 to +0.5 V versus SCE, are presented in Figure  6a-c. Figure 6d demonstrates the areal capacitance obtained for MnFe-9h, MnFe-12h, and MnFe-24h at different scan rates. The highest areal capacitance (capacities) of 1196 mFcm −2 (717 mCcm −2 ), 2013 mFcm −2 (1208 mCcm −2 ), and 1802 mFcm −2 (1081 mCcm −2 ) was achieved at 5mVs −1 , whereas the values of 310 mFcm −2 (186 mCcm −2 ) , 679 mFcm −2 (407 mCcm −2 ), and 474 mFcm −2 (284 mCcm −2 ) for areal capacitance (capacities) were obtained even at a high scan rate of 100 mVs −1 for MnFe-9h, MnFe-12h, and MnFe-24h, respectively. This decrease in capacitance with increasing scan rates is due to the difficulty of diffusing electrolyte ions into the electrodes' internal structure and pores and, hence, the ineffective interaction between electrode and electrolyte occurs. The CV curves of the MnFe-9h, MnFe-12h, and MnFe-24h electrodes recorded with varying scan rates from 5 to 100 mVs −1 , in a potential window of −0.1 to +0.5 V versus SCE, are presented in Figure 6a-c. Figure 6d demonstrates the areal capacitance obtained for MnFe-9h, MnFe-12h, and MnFe-24h at different scan rates. The highest areal capacitance (capacities) of 1196 mFcm −2 (717 mCcm −2 ), 2013 mFcm −2 (1208 mCcm −2 ), and 1802 mFcm −2 (1081 mCcm −2 ) was achieved at 5mVs −1 , whereas the values of 310 mFcm −2 (186 mCcm −2 ), 679 mFcm −2 (407 mCcm −2 ), and 474 mFcm −2 (284 mCcm −2 ) for areal capacitance (capacities) were obtained even at a high scan rate of 100 mVs −1 for MnFe-9h, MnFe-12h, and MnFe-24h, respectively. This decrease in capacitance with increasing scan rates is due to the difficulty of diffusing electrolyte ions into the electrodes' internal structure and pores and, hence, the ineffective interaction between electrode and electrolyte occurs.  Figure 5b displays the GCD curves of the nanoparticles of all MnFe-LDH electrodes. An analogous observation of the electrochemical behavior compared to CV of the electrodes is seen from the GCD measurements. The deviation in triangular shape of the GCD curves for all electrodes was observed, again indicating the charging/discharging process was accompanied by electrochemical oxidation/reduction reactions of MnFe-LDH.
From the GCD curves, the maximum areal capacitance (capacities) of 956 mFcm −2 (525 mCcm −2 ), 1886 mFcm −2 (1037 mCcm −2 ), and 1623 mFcm −2 (893 mCcm −2 ) was achieved at an applied current of 25 mA, for MnFe-9h, MnFe-12h, and MnFe-24h, respectively. The GCD curves measured at different the applied currents of 25, 30, 35, and 40 mA for the MnFe-9h, MnFe-12h, and MnFe-24h electrodes are as presented in Figure 7a-c. Figure 7d represents the obtained areal capacitance at different applied currents for MnFe-9h, MnFe-12h, and MnFe-24h. From the above electrochemical studies, it was found that the MnFe-12h electrode exhibits the maximum capacitance (capacity) from the CV and GCD curves. A maximum areal energy density and a power density of 0.16 mW h cm −2 and 13.75 mW cm −2 , respectively, at an applied current of 25 mA, were achieved.  Figure 5b displays the GCD curves of the nanoparticles of all MnFe-LDH electrodes. An analogous observation of the electrochemical behavior compared to CV of the electrodes is seen from the GCD measurements. The deviation in triangular shape of the GCD curves for all electrodes was observed, again indicating the charging/discharging process was accompanied by electrochemical oxidation/reduction reactions of MnFe-LDH.
All the above obtained results strongly proved the conclusion that the MnFe-LDH's morphological features play a significant role in its electrochemical performance. Initially, for MnFe-9h, the aggregated nanoparticles limit the use of the electrochemically active sites. Likewise, at the maximum hydrothermal reaction time (MnFe-24h), the formation of large leaf-like nanostructures cover the electro-active sites, thus restricting the interaction between the electrolyte and active material. The uniform, thin, and well-organized nanosheets of MnFe-LDH represent an advantageous nanostructure that offers sufficient electrochemical active sites, improves the electrode-electrolyte interface, and hence boosts the redox reaction rate. All the above obtained results strongly proved the conclusion that the MnFe-LDH's morphological features play a significant role in its electrochemical performance. Initially, for MnFe-9h, the aggregated nanoparticles limit the use of the electrochemically active sites. Likewise, at the maximum hydrothermal reaction time (MnFe-24h), the formation of large leaf-like nanostructures cover the electro-active sites, thus restricting the interaction between the electrolyte and active material. The uniform, thin, and well-organized nanosheets of MnFe-LDH represent an advantageous nanostructure that offers sufficient electrochemical active sites, improves the electrode-electrolyte interface, and hence boosts the redox reaction rate.
As shown in the Nyquist plots (Figure 5c), the MnFe-9h, MnFe-12h, and MnFe-24h electrodes form a semicircle in the high-frequency region and an inclined straight line in the low-frequency region. The intersection with the X-axis towards very high frequency in the Nyquist plot estimates the equivalent series resistance (ESR). The radius of the semicircle can define the charge transfer resistance [5]. The ESR values (from Figure 5f) of the MnFe-9h, MnFe-12h, and MnFe-24h electrodes are 0.50, 0.42, and 0.45 Ω, respectively. The radii of the semicircle for MnFe-9h is small (compared to MnFe-12h and MnFe-24h), whereas for the MnFe-12h and MnFe-24h electrodes it is nearly the same. These ESR and charge transfer resistance results suggest the satisfactory electrochemical performance of the MnFe-12h electrode.
To further evaluate the electrochemical performance of the MnFe-12h electrode in a real application, an asymmetrical cell device was assembled using activated carbon as a negative electrode and MnFe-12h as a positive electrode. The CVs of both the AC and MnFe-12h measured in a three-electrode configuration at a 10 mVs −1 scan rate are shown in Figure 8a. The working potentials of the AC and MnFe-12h electrodes were −1.0 to 0 V and −0.1 to 0.5 V versus SCE, respectively, which As shown in the Nyquist plots (Figure 5c), the MnFe-9h, MnFe-12h, and MnFe-24h electrodes form a semicircle in the high-frequency region and an inclined straight line in the low-frequency region. The intersection with the X-axis towards very high frequency in the Nyquist plot estimates the equivalent series resistance (ESR). The radius of the semicircle can define the charge transfer resistance [5]. The ESR values (from Figure 5f) of the MnFe-9h, MnFe-12h, and MnFe-24h electrodes are 0.50, 0.42, and 0.45 Ω, respectively. The radii of the semicircle for MnFe-9h is small (compared to MnFe-12h and MnFe-24h), whereas for the MnFe-12h and MnFe-24h electrodes it is nearly the same. These ESR and charge transfer resistance results suggest the satisfactory electrochemical performance of the MnFe-12h electrode.
To further evaluate the electrochemical performance of the MnFe-12h electrode in a real application, an asymmetrical cell device was assembled using activated carbon as a negative electrode and MnFe-12h as a positive electrode. The CVs of both the AC and MnFe-12h measured in a three-electrode configuration at a 10 mVs −1 scan rate are shown in Figure 8a. The working potentials of the AC and MnFe-12h electrodes were −1.0 to 0 V and −0.1 to 0.5 V versus SCE, respectively, which indicates that the operating cell voltage of the MnFe-12h//AC can be 1.6 V. The mass deposited on both the conductors was determined using the charge matching method represented as Q + = Q − , where Q + and Q − are the positive and negative electrode charges, respectively [29]. Based on this, the mass loading on the positive electrode is 1.1 mg, whereas it is 2.1 mg on negative electrode, with a mass ratio of 0.52. To determine the operating voltage window, the CV curves of the MnFe-12h//AC asymmetric cell device were measured with an increasing voltage window (from 0-0.3 to 0-1.7 V) as illustrated in Figure 8b. When increasing the voltage to 1.7 V, some discrete redox peaks were seen, designating deeper redox reactions on the surface of the MnFe-LDH nanosheets. From this, the appropriate voltage window of 0-1.6 V was achieved for the MnFe-12h//AC asymmetric cell device; beyond this value, polarization becomes visible. Figure 8c shows the CV curves of the MnFe-12h//AC asymmetric cell device recorded at scan rates from 10 mVs −1 to 100 mVs −1 within the optimized voltage window of 0 to 1.6 V. The areal capacitance (capacities) of the MnFe-LDH nanosheets increased from 226 mFcm −2 (68 mCcm −2 ) with a voltage window of 0-0.3 V to 3915 mFcm −2 (6264 mCcm −2 ) with a voltage window of 0-1.6 V, at a scan rate of 10 mVs −1 for the MnFe-12h//AC asymmetric cell device. A maximum areal capacitance (capacities) of 3915 mFcm −2 (6264 mCcm −2 ) at 10 mVs −1 was achieved, whereas 1354 mFcm −2 (2166 mCcm −2 ), even at a high scan rate 100 mVs −1 , was achieved from the MnFe-12h//AC asymmetric cell device. ratio of 0.52. To determine the operating voltage window, the CV curves of the MnFe-12h//AC asymmetric cell device were measured with an increasing voltage window (from 0-0.3 to 0-1.7 V) as illustrated in Figure 8b. When increasing the voltage to 1.7 V, some discrete redox peaks were seen, designating deeper redox reactions on the surface of the MnFe-LDH nanosheets. From this, the appropriate voltage window of 0-1.6 V was achieved for the MnFe-12h//AC asymmetric cell device; beyond this value, polarization becomes visible. Figure 8c shows the CV curves of the MnFe-12h//AC asymmetric cell device recorded at scan rates from 10 mVs −1 to 100 mVs −1 within the optimized voltage window of 0 to 1.6 V. The areal capacitance (capacities) of the MnFe-LDH nanosheets increased from 226 mFcm −2 (68 mCcm −2 ) with a voltage window of 0-0.3 V to 3915 mFcm −2 (6264 mCcm −2 ) with a voltage window of 0-1.6 V, at a scan rate of 10 mVs −1 for the MnFe-12h//AC asymmetric cell device. A maximum areal capacitance (capacities) of 3915 mFcm −2 (6264 mCcm −2 ) at 10 mVs −1 was achieved, whereas 1354 mFcm −2 (2166 mCcm −2 ), even at a high scan rate 100 mVs −1 , was achieved from the MnFe-12h//AC asymmetric cell device. The GCD curves of the MnFe-12h//AC asymmetric cell also recorded with different applied voltage windows (from 0-0.3 to 0-1.6 V) are presented in Figure 8d. This figure displays the GCD curves of the MnFe-12h//AC asymmetric cell device measured at applied currents from 10 mA to 30 mA. Little variation in the triangular shape of the GCD curves again represents the occurrence of redox reactions on the surface of the MnFe-LDH nanosheets. The MnFe-12h//AC asymmetric cell device delivers a maximum areal capacitance (capacity) of 506 mFcm −2 (809 mCcm −2 ), with an energy density of 44.9 µW h cm −2 , and a power density of 16 mW cm −2 at an applied current of 10 mA, within the 1.6 V operating voltage window.
The specific energy and power densities of the MnFe-12h//AC asymmetric cell device obtained at different applied currents are shown in the Ragone plot in Figure 9a. The MnFe-12h//AC asymmetric cell device delivers a maximum specific energy density of 55.01 W h kg −1 , with a power density of 5000 W kg −1 at an applied current of 10 mA, within the 1.6 V operating voltage window. The GCD curves of the MnFe-12h//AC asymmetric cell also recorded with different applied voltage windows (from 0-0.3 to 0-1.6 V) are presented in Figure 8d. This figure displays the GCD curves of the MnFe-12h//AC asymmetric cell device measured at applied currents from 10 mA to 30 mA. Little variation in the triangular shape of the GCD curves again represents the occurrence of redox reactions on the surface of the MnFe-LDH nanosheets. The MnFe-12h//AC asymmetric cell device delivers a maximum areal capacitance (capacity) of 506 mFcm −2 (809 mCcm −2 ), with an energy density of 44.9 µW h cm −2 , and a power density of 16 mW cm −2 at an applied current of 10 mA, within the 1.6 V operating voltage window.
The specific energy and power densities of the MnFe-12h//AC asymmetric cell device obtained at different applied currents are shown in the Ragone plot in Figure 9a. The MnFe-12h//AC asymmetric cell device delivers a maximum specific energy density of 55.01 W h kg −1 , with a power density of 5000 W kg −1 at an applied current of 10 mA, within the 1.6 V operating voltage window. The specific energy density and power density values attained in the present study for the MnFe-12h//AC asymmetric cell device are higher than those of previously reported studies for an LDH-based asymmetric cell device, which are depicted in the Ragone plot (Figure 9a) [23,[30][31][32][33][34][35][36][37][38][39]. To assess the electrochemical stability, the long-term performance of the MnFe-12h//AC asymmetric cell device was investigated by CV measurements for 5000 cycles at a scan rate of 10 mVs −1 . Figure 9b presents the effect on capacitance retention and areal capacitance of the MnFe-12h//AC device with increasing electrochemical cycle numbers. The inset of Figure 9b presents the CV recorded for the 1st and 5001st electrochemical cycles for the MnFe-12h//AC device at a scan rate of 10 mVs −1 . The small variation in the CV curve was observed after performing 5000 cycles, suggesting the slight change in electrochemical performance after performing 5000 cycles. The MnFe-12h//AC cell device exhibited a capacitance retention of approximately 93%, with an areal capacitance of approximately 3641 mFcm −2 , after 5000 cycles, suggesting an excellent and stable electrochemical performance.
the electrochemical stability, the long-term performance of the MnFe-12h//AC asymmetric cell device was investigated by CV measurements for 5000 cycles at a scan rate of 10 mVs −1 . Figure 9b presents the effect on capacitance retention and areal capacitance of the MnFe-12h//AC device with increasing electrochemical cycle numbers. The inset of Figure 9b presents the CV recorded for the 1st and 5001st electrochemical cycles for the MnFe-12h//AC device at a scan rate of 10 mVs −1 . The small variation in the CV curve was observed after performing 5000 cycles, suggesting the slight change in electrochemical performance after performing 5000 cycles. The MnFe-12h//AC cell device exhibited a capacitance retention of approximately 93%, with an areal capacitance of approximately 3641 mFcm −2 , after 5000 cycles, suggesting an excellent and stable electrochemical performance. The typical Nyquist plots for the AC//MnFe-12h asymmetric cell device before and after performing 5000 cycles are presented in Figure 8f. These Nyquist plots again designate the semicircle toward the high-frequency region and the vertical straight line in the low-frequency region, further suggesting the ideal supercapacitor behavior of the AC//MnFe-12h asymmetric cell device. The inset of Figure 8f shows the magnified view of the Nyquist plots, denoting the low ESR values, namely The typical Nyquist plots for the AC//MnFe-12h asymmetric cell device before and after performing 5000 cycles are presented in Figure 8f. These Nyquist plots again designate the semicircle toward the high-frequency region and the vertical straight line in the low-frequency region, further suggesting the ideal supercapacitor behavior of the AC//MnFe-12h asymmetric cell device. The inset of Figure 8f shows the magnified view of the Nyquist plots, denoting the low ESR values, namely 0.26 and 0.28 Ω before and after performing 5000 cycles, respectively. There was a small distinction perceived in the Nyquist plots with a very small change in ESR values (0.02 Ω) for the AC//MnFe-12h asymmetric cell device after performing 5000 electrochemical cycles, indicating the good stability of the assembled cell device.

Conclusions
In the present study, we modified the morphological features of MnFe-LDH using the hydrothermal method and examined in detail its supercapacitive electrochemical performance. Our results reveal that the uniform and well-organized MnFe-LDH nanosheets obtained after the 12 h hydrothermal reaction time afford several active electrochemical sites, effective access to the electrolyte ions, and a minimum resistance path, boosting the electrochemical redox reactions and, hence, enhancing the electrochemical properties. The MnFe-12h//AC asymmetric cell device delivers a maximum capacitance of 506 mFcm −2 , with an energy density of 44.9 µW h cm −2 (55.01 W h kg −1 ) and a power density of 16 mW cm −2 (5000 W kg −1 ) at an applied current of 10 mA, (with 93% capacitance retention after performing 5000 cycles, at 10 mVs −1 ) within the 1.6 V operating voltage window. These encouraging electrochemical characteristics of MnFe-LDH nanosheets offer its feasible use as an electrode material for an efficient energy storage device.