Waste Citrus reticulata Assisted Preparation of Cobalt Oxide Nanoparticles for Supercapacitors

The green, sustainable, and inexpensive creation of novel materials, primarily nanoparticles, with effective energy-storing properties, is key to addressing both the rising demand for energy storage and the mounting environmental concerns throughout the world. Here, an orange peel extract is used to make cobalt oxide nanoparticles from cobalt nitrate hexahydrate. The orange peel extract has Citrus reticulata, which is a key biological component that acts as a ligand and a reducing agent during the formation of nanoparticles. Additionally, the same nanoparticles were also obtained from various precursors for phase and electrochemical behavior comparisons. The prepared Co-nanoparticles were also sulfurized and phosphorized to enhance the electrochemical properties. The synthesized samples were characterized using scanning electron microscopic and X-ray diffraction techniques. The cobalt oxide nanoparticle showed a specific capacitance of 90 F/g at 1 A/g, whereas the cobalt sulfide and phosphide samples delivered an improved specific capacitance of 98 F/g and 185 F/g at 1 A/g. The phosphide-based nanoparticles offer more than 85% capacitance retention after 5000 cycles. This study offers a green strategy to prepare nanostructured materials for energy applications.


Introduction
The demand for energy leads to the continuous depletion of fossil fuels. Today, due to the requirement for a large amount of energy, scientists tend to move toward the storage application with the help of energy storage devices (ESDs). ESDs are widely used in transportation and large-scale industries. There are various types of ESDs, such as batteries [1], fuel cells [2], and supercapacitors (SCs) [3]. Among these devices, batteries have the highest number of users due to their high energy density and large cyclability. However, their low power density allows researchers to look for alternative solutions, i.e., fuel cells that store green energy in the form of hydrogen and are currently in the developing face, which may enter the market soon. Moreover, the SCs of these ESDs have high power density and can be used where power density is required. There are various types of SCs. Based on the principle of energy storage mechanism, they are of two types: one electric double-layer capacitance (EDLCs) and pseudocapacitor [4]. The EDLC stores energy through electrostatic interaction between the ions, forming the double layer on the electrode surface [5]. The pseudocapacitor stores charges through the electrochemical

Preparation of Peel Extracts
To make an extract, orange fruits were washed and left to dry at room temperature before being peeled. The collected peels were placed in an oven at 60 • C overnight. The fine powder was obtained after grinding a dried peel. Next, 2 g of powdered peel were dissolved in 50 mL of DI water and stirred for 3 h at room temperature. Afterward, the mixture was placed in a water bath at 60 • C for 60 min. In the end, the mixture was filtered, and the supernatant was collected to further synthesize metal oxide nanoparticles.

Synthesis of CoO/Co 3 O 4 Nanoparticles
Typically, 2 g of Co(NO 3 ) 2 .6H 2 O were dissolved into 42.5 mL of the as-prepared above peel extract and stirred at room temperature for 60 min. The beaker was transferred to a water bath at 60 • C for 1 h. Further, the mixture was dried overnight at 60 • C. The obtained CoO was ground into fine powder and it was characterized later. CoO is referred to as CoO-OP. To prepare the Co 3 O 4 phase of cobalt oxide, a half of the sample was calcined at 400 • C at 5 deg./min. The nanoparticles obtained by heat treatment were labeled as Co 3 O 4 -OP-C. Hence the cobalt oxide nanoparticles were obtained using orange peels as a reducing ligand.

Synthesis of Cobalt Oxide Using NaOH
The Co(NO 3 ) 2 ·6H 2 O (2 g) was poured into 40 mL of (1N) NaOH and stirred for 60 min. The beaker was placed in a water bath at 60 • C for 1 h. The mixture was dried overnight at 60 • C. Hence Co 3 O 4 particles were obtained without calcination and characterized. The peel extract reducing agent was replaced with NaOH to facilitate the comparative study of the phases. Hence, the obtained cobalt oxide nanoparticles using NaOH (Co 3 O 4 -NaOH) were referred to as a reference nanoparticle for the study.

Sulfurization
The sulfurized cobalt oxide nanoparticles were synthesized by dissolving Na 2 S 2 O 3 ·5H 2 O with the already prepared CoO-OP nanoparticles, according to a ratio of 1:10 in water and transferred to the Teflon-lined autoclave (45 mL) under 160 • C for 24 h, then cooled down at room temperature. Further, the obtained material was washed several times with DI water and ethanol, placed to centrifugation for 10 min, and kept for drying in an oven at 70 • C overnight. The dried sample was taken out and ground to an exceptionally fine powder, and hence cobalt sulfide nanoparticles were formed. The Co 2 S phase was obtained from the CoO-OP and referred to as CoO-S-OP. Therefore, the same steps were used to prepare the Co 3 S 4 phase from an annealed sample of Co 3 O 4 -OP-C, which is referred to as Co 3 O 4 -S-OP-C, and Co 3 S 4 -S-NaOH was obtained from Co 3 O 4 -NaOH.

Phosphorization
NaPO 2 H 2 .H 2 O in one ceramic dish and the already prepared CoO-OP NPs in another dish were taken and annealed at 350 • C in a tube furnace for 5 h under the presence of Argon (Ar) atmosphere with a heating rate of 5 • C/min. The cobalt phosphide NPs (CoP) were obtained. The CoP phase was obtained for all the samples. The CoO-P-OP, Co 3 O 4 -P-OP-C, and Co 3 O 4 -P-NaOH are referred for CoO-OP, Co 3 O 4 -OP-C, and Co 3 O 4 -NaOH nanoparticles, respectively. The schematic diagram of the synthesis of nanoparticles is provided in Figure 1 along with the proposed mechanism of the synthesis of the cobalt oxide nanoparticles by using peel extract. The presence of hydroxide (-OH) in the peel powder helps as a capping agent and as a possible reaction mechanism for the preparation of the metal oxide nanoparticles using orange peel extract in which ligation takes place between the functional components of the orange peel and cobalt precursor [29]. Organic substances such as flavonoids, limonoids, and carotenoids are present in orange peel extract, which acts as a ligand agent. One of the extract component's hydroxyl aromatic ring groups reacts with a precursor and forms a complex-ligand with Co ions. Chemical reactions such as nucleation and shaping help in the formation of stabilized nanoparticles. Then the mixture of the organic solution is decomposed, the precipitate is calcined in the presence of air, and cobalt oxide nanoparticles are released [30]. OP-C, and Co3O4-P-NaOH are referred for CoO-OP, Co3O4-OP-C, and Co3O4-NaOH nanoparticles, respectively. The schematic diagram of the synthesis of nanoparticles is provided in Figure 1 along with the proposed mechanism of the synthesis of the cobalt oxide nanoparticles by using peel extract. The presence of hydroxide (-OH) in the peel powder helps as a capping agent and as a possible reaction mechanism for the preparation of the metal oxide nanoparticles using orange peel extract in which ligation takes place between the functional components of the orange peel and cobalt precursor [29]. Organic substances such as flavonoids, limonoids, and carotenoids are present in orange peel extract, which acts as a ligand agent. One of the extract component's hydroxyl aromatic ring groups reacts with a precursor and forms a complex-ligand with Co ions. Chemical reactions such as nucleation and shaping help in the formation of stabilized nanoparticles. Then the mixture of the organic solution is decomposed, the precipitate is calcined in the presence of air, and cobalt oxide nanoparticles are released [30].

Physicochemical Characterization
The successful preparation of the cobalt oxide nanoparticles by using orange peel extract and NaOH was followed by phosphorization and sulfurization. Hence, the surface morphology of the prepared samples was characterized by scanning electron microscopy (SEM) (at 10 keV). X-Ray diffraction was used to study the phase purity using a Lab X (XRD-6000) Shimadzu X-ray diffractometer employing Cu Kα radiative instrument. To investigate insights into the structure and morphology of the particles of the synthesized materials, SEM was conducted and showed the surface structure of the materials at the scale of 200 nm. We could see the irregular sponge-like structure with the uneven pore size distributed nonuniformly throughout the CoO-OP (Figure 2a). By contrast, the sponge-like structure appears in the Co3O4-OP-C ( Figure 2b) with smaller pores than the CoO-OP. However, the zig-zag continuous flakes were observed in the Co3O4-NaOH (Figure 2c) precursor. Sulfurization and phosphorization adversely affect the morphology of the material. Hence, the sponge-like morphology changed into small globular-like clouds, as is observed in Figure 2d of the CoO-S-OP. Figure 2e demonstrates the uneven open flower-like structure for the Co3O4-S-OP-C. However, a dense granular structure was observed in the Co3O4-S-NaOH ( Figure 2f) and Co3O4-P-NaOH (Figure 2i). The web-

Physicochemical Characterization
The successful preparation of the cobalt oxide nanoparticles by using orange peel extract and NaOH was followed by phosphorization and sulfurization. Hence, the surface morphology of the prepared samples was characterized by scanning electron microscopy (SEM) (at 10 keV). X-ray diffraction was used to study the phase purity using a Lab X (XRD-6000) Shimadzu X-ray diffractometer employing Cu K α radiative instrument. To investigate insights into the structure and morphology of the particles of the synthesized materials, SEM was conducted and showed the surface structure of the materials at the scale of 200 nm. We could see the irregular sponge-like structure with the uneven pore size distributed nonuniformly throughout the CoO-OP (Figure 2a). By contrast, the sponge-like structure appears in the Co 3 O 4 -OP-C ( Figure 2b) with smaller pores than the CoO-OP. However, the zig-zag continuous flakes were observed in the Co 3 O 4 -NaOH (Figure 2c) precursor. Sulfurization and phosphorization adversely affect the morphology of the material. Hence, the sponge-like morphology changed into small globular-like clouds, as is observed in Figure 2d of the CoO-S-OP. Figure [31]. The sample Co3O4-OP-C and Co3O4-NaOH signify a face-centered cubic structure. The obtained crystalline structure of the Co3O4 phase has a lattice constant of a = 8.076 Å and a space group of Fd3m. The Debye-Scherrer equation was used for the calculation of the average particle size: DXRD = 0.9λ/(βcosθ) where DXRD is the average crystalline size, λ is the wavelength of Cu-Kα, β is the full width at half maximum (FWHM) of the diffraction peak and θ is the Bragg's angle. Furthermore, after the sulfurization process, the peaks of the CoS2 phase were observed for the CoO-S-OP. The main characteristic peaks and relative intensities match significantly with (210), (211), and (230) shown in Figure 3d as JCPDS No. 41-1471. The dimmer is formed by sulfur atoms covalently, and the divalent Co 2+ cation is placed in the center of an octahedron of six S2 2-anions. Hence each sulfur is incorporated into three different octahedra and a single dimmer. Therefore, the CoO-S-OP showed an octahedral crystal structure [32].
Figure 3e,f show a typical XRD pattern of the as-prepared Co3O4-S-OP-C and Co3O4-S-NaOH samples, which represents the Co3S4 phase with the standard pattern of JCPDS No. 42-1448 at 2θ = 31.4º, 36.5º, 37.02º, 38.7º, 44.8º, and 59.4º, and corresponds to the (220),  [31]. The sample Co 3 O 4 -OP-C and Co 3 O 4 -NaOH signify a face-centered cubic structure. The obtained crystalline structure of the Co 3 O 4 phase has a lattice constant of a = 8.076 Å and a space group of Fd3m. The Debye-Scherrer equation was used for the calculation of the average particle size: D XRD = 0.9λ/(βcosθ) where D XRD is the average crystalline size, λ is the wavelength of Cu-Kα, β is the full width at half maximum (FWHM) of the diffraction peak and θ is the Bragg's angle. Furthermore, after the sulfurization process, the peaks of the CoS 2 phase were observed for the CoO-S-OP. The main characteristic peaks and relative intensities match significantly with (210), (211), and (230) shown in Figure 3d as JCPDS No. 41-1471. The dimmer is formed by sulfur atoms covalently, and the divalent Co 2+ cation is placed in the center of an octahedron of six S 2 2− anions. Hence each sulfur is incorporated into three different octahedra and a single dimmer. Therefore, the CoO-S-OP showed an octahedral crystal structure [32]. pattern of CoP cited at 31.6º, 36.3º, 46.2º, 48.1º and 56.7º can be evaluated as the (011), (111), (112), (211), and (301) planes (JCPDS 29-0497), which showed an orthorhombic crystal geometry [36]. The CoP phase (a = 5.08 (2), b = 3.282(11), c = 5.66(2) Å) includes a nanocrystalline and P deficient domain. Therefore, the structure of CoP distorted to octahedral and shows an octahedral connectivity around Co.

Electrochemical Testing
The electrochemical measurements were carried out at room temperature using a three-electrode system using a Versa stat 4-500 electrochemical workstation (Princeton Applied Research, TN, USA). The supercapacitor performance was analyzed through   [33][34][35]. As the phosphorization reaction happens from the surface, the obtained products are most likely to be inhomogeneous because of the reaction surface area in the crystal architecture. The development of domains such as the CoP (Co + and P − ) phase was examined. Moreover, the rationalized phase was balanced with the valence states of the Co ions and the available amount of phosphorus (P). The product's crystal anatomy was determined by XRD in Figure 3g , which showed an orthorhombic crystal geometry [36]. The CoP phase (a = 5.08 (2), b = 3.282 (11), c = 5.66 (2) Å) includes a nanocrystalline and P deficient domain. Therefore, the structure of CoP distorted to octahedral and shows an octahedral connectivity around Co.

Electrochemical Testing
The electrochemical measurements were carried out at room temperature using a three-electrode system using a Versa stat 4-500 electrochemical workstation (Princeton Applied Research, TN, USA). The supercapacitor performance was analyzed through cyclic voltammetry (CV) and galvanostatic charge-discharge (CD), and electrochemical impedance spectroscopy (EIS) and stability were performed to record the best outcome for the specific capacitance among the synthesized nanoparticles in a 3 M KOH solution. Electrochemical characterization was stabilized by accounting for a three-electrode system. For supercapacitor tests, a saturated mercury/mercury oxide (Hg/HgO), platinum (Pt), and the synthesized material on Ni foam were used as a reference electrode, counter electrode, and working electrode, respectively. The electrochemical performance and specific capacitance of the Ni foam loaded with the prepared NPs electrodes were investigated in the operating voltage window of 0-0.6 V.
Electrodes were prepared in the consideration of the set standard parameters for electrochemical testing. The prepared samples PVDF: NMP were taken in the ratio of 8:1:1 to form the slurry, where PVDF is poly-vinyl di-fluoride and NMP refers to n-methyl polypropylene. The already-prepared slurry was spread uniformly on the Ni foam via dipping and then transferred to the vacuum and dried at 70 • C for 48 h. The active mass loading of the best sample (CoO-P-OP) is 2.61 mg. The faradic redox curves were obtained through CV testing, which indicates the pseudocapacitive and/or EDLC behavior. EDLC indicates the adsorption or desorption mechanism during the charge storage in the pseudocapacitive behavior of the cobalt oxide nanoparticles, in addition to the excellent capacitive retention, with a rate of more than 80% from 2 to 300 mV/s. The samples explain the pseudocapacitive traits, which are confirmed by the pair of redox peaks at each scan rate. As noticed, the area of the CV curve increases with the increase in the scan rate, which justified the diffusion-controlled reaction kinetics and has two sets of redox peaks. Hence, the possible faradaic reactions for the CoO-OP can be obtained by Equations (1) and (2) [37], and those for Co 3 O 4 -OP-C and Co 3 O 4 -NaOH can be obtained with Equations (3) and (4) [38], which are arbitrated by OH − ions in the alkaline medium: A better rate performance than the CoO-OP, Co 3 O 4 -OP-C, and Co 3 O 4 -NaOH was observed by the sulfurized nanoparticles. Therefore, the shape of the CV curve in Figure 4a-f and Figures S1-S3 is maintained by two pairs of notable redox reactions; significant peaks were noticed in the CV curves, which may occur due to the quasi-reversible [39] electron transfer processes of Co 2+ ↔ Co 3+ and Co 3+ ↔ Co 4+ within the electroactive materials. Thus, most reported cobalt sulfides show pseudocapacitive traits. The redox reaction for the CoO-S-OP is indicated in Equations (5) and (6) (7) and (8) [41]. The proposed redox reactions for the CoO-P-OP, Co3O4-P-OP-C, and Co3O4-P-NaOH are indicated in Equations (9)-(12) [42], which are based on the CV curve. The CoO-P-OP, Co3O4-P-OP-C, and Co3O4-P-NaOH showed the same CoP phase in XRD (Figure 3g-i). According to the already reported results on the CoP phase, the material for supercapacitor exhibits the overall redox reaction (Equations (9)-(12)), which is caused by the Co(OH)2 that is obtained due to oxidation of CoP phase at low voltage and the CoxPyOz surface formed due to chemical reaction. Furthermore, it is recorded that CoP exhibits comparable much higher current densities than other samples in the literature for phosphorized cobalt oxide. Element P was lost after the stability test and P might transfer into PO4 3− and mixed in water [43].

[40]; Co 3 O 4 -S-OP-C and Co 3 O 4 -S-NaOH are indicated in Equations
CoP + 2OH ⇌ Co(OH) + P + 2e (9) Co(OH) + OH ⇌ CoOOH + H O + 2e (10) CoOOH + OH ⇌ CoO + H O + e (11) Co P O + OH ⇌ Co P O OH + e (12) Moreover, there is no drastic change in the shape of the CV curves at various current densities, which indicates the best reversibility with enhanced mass transportation. The phosphorized samples have a larger area under the CV curves, which indicates a higher ability to store charges. Furthermore, as noticed, the area of the CV curve increases with The proposed redox reactions for the CoO-P-OP, Co 3 O 4 -P-OP-C, and Co 3 O 4 -P-NaOH are indicated in Equations (9)-(12) [42], which are based on the CV curve. The CoO-P-OP, Co 3 O 4 -P-OP-C, and Co 3 O 4 -P-NaOH showed the same CoP phase in XRD (Figure 3g-i). According to the already reported results on the CoP phase, the material for supercapacitor exhibits the overall redox reaction (Equations (9)-(12)), which is caused by the Co(OH) 2 that is obtained due to oxidation of CoP phase at low voltage and the Co x P y O z surface formed due to chemical reaction. Furthermore, it is recorded that CoP exhibits comparable much higher current densities than other samples in the literature for phosphorized cobalt oxide. Element P was lost after the stability test and P might transfer into PO 4 3− and mixed in water [43].
Moreover, there is no drastic change in the shape of the CV curves at various current densities, which indicates the best reversibility with enhanced mass transportation. The phosphorized samples have a larger area under the CV curves, which indicates a higher ability to store charges. Furthermore, as noticed, the area of the CV curve increases with the increase in the scan rate, which justified the diffusion-controlled reaction kinetics and holds two sets of redox peaks. The following equation was used to study the charge storage mechanism (Equation (13)) [44]. i = av b (13) where i is the measure of peak current, v is scan rate, and a and b are the parameters. The charge storage mechanism is influenced by the diffusion-controlled faradic reaction if b is 0.5, and when b is 1 the total charge performance is affected by the capacitive surface mechanism. Figure 4g displays the slope of the three best samples out of the nine synthesized samples; the CoO-OP, CoO-S-OP, and CoO-P-OP electrodes' b value is 0.83, 0.71, and 0.81, respectively. These obtained values indicate that the electrodes have a hybrid charge storage mechanism and it was observed in detail by using the following equation (Equation (14)) [44], in which k 1 v is the capacitive effect and k 2 v 1/2 is the diffusioncontrolled effects.
In Figure 4h,i, both the traits were analyzed at 5 mV/s and 100 mV/s scan rates. At a low scan rate (5 mV/s), the diffusion and capacitance contributions were 77% and 23%, 87% and 13%, and 82% and 18%, respectively. However, at a high scan rate (100 mV/s), these contributions were 62% and 38%, 61% and 39%, and 50% and 50% for the CoO-OP, CoO-S-OP, and CoO-P-OP electrodes, respectively. Higher specific capacitance is due to a diffusion-controlled reaction in which the electrolyte penetrates the deep nanomaterial interlayers. On the other hand, at a higher scan rate, the electrodes possessed a lower specific capacitance, which may be because of the surface phenomenon. SEM of the CoO-P-OP (Figure 2g) showed a more porous structure with the thin wires which gives the shape of a web, and this increases the active surface sites for the ions to penetrate inside the material. Furthermore, the electrochemical performance of the CoO-P-OP is better than the CoO-S-OP and CoO-OP, which can be reasoned to the lower electronegativity of P, and the ability to fit in the interstitial position between the metal atoms. Due to its optimum size, it behaves as a site of a positive radical and is rich in holding and entangling positive species [45]. However, the associated metal behaves as an electropositive and traps the lone pair species or electrons. Therefore, the introduction of P in a cobalt oxide nanoparticle can probably enhance its electrochemical activity [46].
All the samples showed good symmetry and high coulombic efficiency because of the diffusion-controlled phenomenon during the faradic electron transfer with a fast reaction rate and less time for the electrons to couple; and due to polarization, the reduction peaks shift swiftly to the left, which resembled the high scan rate [47]. On the other hand, the oxidation peaks shift toward the right. The high scan rate of the current is recorded for the phosphorized samples among all because the electrons took less time to emit and absorb, which resulted in the peak shifting and fast scan rate. Moreover, the highest surface area noticed in the phosphorized electrodes of the CV curves indicates their ability to store a greater amount of charge for the higher specific capacitance. The above fact is further confirmed by the GCD curves (Figure 5a-i), where the discharge time is related to a specific capacitance, which means that the longer the discharge time, the higher the specific capacitance. The relation is given below (Equation (15)) [48,49]: Herein, C is the specific capacitance (F/g), I is the current (A), ∆t is the discharge time (s), m is the mass of the active material (g) and ∆V is the potential window.
The GCD for all the samples are performed at various current density ranging from 1 A/g to 30 A/g in the potential range from 0 to 0.6 V. Multiple charge and discharge experiments were carried out. Among all the samples, the noticeable specific capacitance was recorded for the CoO-P-OP as 185 F/g at 1 A/g. The charge-discharge curve delineates that the material is stable up to 5000 charge and discharge cycles. All the synthesized materials showed stable charge-discharge properties, and the nature was asymmetric. Zhou et. al. [43] studied the electrochemical study of the phosphorized materials and observed a couple of distinct faradaic peaks that define the existence of redox behavior in the electrochemical process because of the conversion of Ni (δ+) /Co (δ+) into the Ni (2+) /Co (2+) state in NiCoP/C, Ni 2 P/C and Co 2 P/C. Moreover, the small separation between the anodic and cathodic peaks was observed and indicated the good electrochemical reversibility of the composites. Therefore, the GCD curve has a consistent potential with the CV curves due to polarization, and hence they provide an enhanced specific capacitance. Similarly, the change of the valence state might cause the phosphorized sample to produce effective results for higher capacitance in this study too. The GCD for all the samples are performed at various current density ranging from 1 A/g to 30 A/g in the potential range from 0 to 0.6 V. Multiple charge and discharge experiments were carried out. Among all the samples, the noticeable specific capacitance was recorded for the CoO-P-OP as 185 F/g at 1 A/g. The charge-discharge curve delineates that the material is stable up to 5000 charge and discharge cycles. All the synthesized materials showed stable charge-discharge properties, and the nature was asymmetric. Zhou et. al. [43] studied the electrochemical study of the phosphorized materials and observed a couple of distinct faradaic peaks that define the existence of redox behavior in the electrochemical process because of the conversion of Ni (δ+) /Co (δ+) into the Ni (2+) /Co (2+) state in NiCoP/C, Ni2P/C and Co2P/C. Moreover, the small separation between the anodic and cathodic peaks was observed and indicated the good electrochemical reversibility of the composites. Therefore, the GCD curve has a consistent potential with the CV curves due to polarization, and hence they provide an enhanced specific capacitance. Similarly, the change of the valence state might cause the phosphorized sample to produce effective results for higher capacitance in this study too. In addition, to examine the interfacial electrochemical behaviors of the Ni foam-based electrodes, EIS was measured, which incorporates the information about the resistance offered by the material during the charge transfer. The EIS test was carried out to observe the Nyquist plots from which the impedance data were analyzed and showed a semicircle in the high-frequency range followed by a straight line in the low-frequency range, designating that the electrochemical process on the surface of the material of the electrode is kinetically diffusion administered. The curve can be disintegrated into three parts. The intersection with the x-coordinate in the high-frequency range refers to the electrolyte resistance (R s ), which defines the ionic resistance of the electrolyte, the intrinsic resistance of the electrode, and the interface resistance. The charge transfer resistance (R ct ) is deduced from the diameter of the semicircle. The plots are shown in Figure 6a, and the values of R s and R ct for the fabricated electrodes are shown in Table 1.
electrode is kinetically diffusion administered. The curve can be disintegrated into three parts. The intersection with the x-coordinate in the high-frequency range refers to the electrolyte resistance (Rs), which defines the ionic resistance of the electrolyte, the intrinsic resistance of the electrode, and the interface resistance. The charge transfer resistance (Rct) is deduced from the diameter of the semicircle. The plots are shown in Figure 6a, and the values of Rs and Rct for the fabricated electrodes are shown in Table 1.  The CoO-P-OP and Co3O4-P-OP-C displayed the approximately similar and smallest Rs value detecting the high conductivity. However, the CoO-P-OP showed the least value of Rct of 1.52 Ω among all the synthesized samples, indicating a low-charge transfer hindrance and promoting more movement of electrons. Therefore, the highest specific capacitance is noticed for CoP 185 F/g at 1 A/g because of the doping of P in the already prepared CONPs, which is derived by using peel extract, and the low Csp of the CoO-OP, Co3O4-OP-C, and Co3O4-NaOH may be attributed to its structure loss in the electrolytic system during the electrochemical study. The specific capacitance is illustrated in Figure  6b. Moreover, it improved its energy and power density (Figure 6c). The energy density and power density are derived from Equations (16) and (17) [50,51,52]:  The CoO-P-OP and Co 3 O 4 -P-OP-C displayed the approximately similar and smallest R s value detecting the high conductivity. However, the CoO-P-OP showed the least value of R ct of 1.52 Ω among all the synthesized samples, indicating a low-charge transfer hindrance and promoting more movement of electrons. Therefore, the highest specific capacitance is noticed for CoP 185 F/g at 1 A/g because of the doping of P in the already prepared CONPs, which is derived by using peel extract, and the low C sp of the CoO-OP, Co 3 O 4 -OP-C, and Co 3 O 4 -NaOH may be attributed to its structure loss in the electrolytic system during the electrochemical study. The specific capacitance is illustrated in Figure 6b. Moreover, it improved its energy and power density (Figure 6c). The energy density and power density are derived from Equations (16) and (17) [50][51][52]: The energy density of the CoO-P-OP can approach about 9 Wh/kg at a power density of 296 W/kg. The comparison data between C sp , the power density, and the energy density of all the synthesized samples are illustrated in Table S1 in the Supplementary Information. In addition, the cycling performance was investigated at a current density of 10 A/g for 5000 cycles, the retention capacity of all the samples maintaining at around 85%. Figure 6d shows the retention capacity of the CoO-P-OP, which has the highest specific capacitance with the 5 cycles at the beginning and end to show the consistency of the charge-discharge effect. Better electrical conductivity results in low resistivity, which implies better change transfer and hence enhances the capacitance of a material. Therefore, the CoO-P-OP showed improved results among the other synthesized samples. Table 2 shows the comparison between our sample and some other work.

Conclusions
To recapitulate, this work deals with the green route of synthesis, and the further produced NPs are followed by phosphorization and sulfurization to test the comparative study of the phases and the electrochemistry. Orange peel is a bio-waste material, and the waste was utilized in this study as a reducing agent. Co-nanoparticles were produced by the precipitation method. The crystalline quality with the well-defined peaks and structural history was recorded by XRD. All samples were tested for supercapacitor study and all phosphorized samples showed better electrical conductivity, which results in a bountiful specific capacitance because of the low EIS, a high area in the CV curve, and the high discharge time, recorded in the GCD plots. The synthesized nanoparticles, by using plants, showed the best results and observed a good columbic efficiency, energy, and power density. The stability of the materiassl is consistent and impactful by 85% and the cycles from the beginning and end follow the same trend, hence proving that the nanoparticles derived by using biomaterial are more stable and sustainable.
There is an enormous scope for improving the capacitive property of the metal oxide nanoparticles by using plant extracts such as the incorporation of carbon quantum dots in making composites, reduced graphene, MXenes, phosphides and sulfides for the improvement of the supercapacitive attributes, and research in this direction would evolve a plethora of significant materials for supercapacitors.
Supplementary Materials: The following supporting information can be downloaded at: https: //www.mdpi.com/article/10.3390/nano12234119/s1. Figure S1: The CV scan curve from 2 to 300 mV/s for prepared (a) CoO-OP; Figure S2: The CV scan curve from 2 to 300 mV/s for prepared (b) Co3O4-OP-C; Figure S3: The CV scan curve from 2 to 300 mV/s for prepared (c) Co3O4-NaOH; Table S1: The comparison between specific capacitance (Csp), power density, and energy density of the synthesized samples.

Conflicts of Interest:
The authors do not have any conflict of interest.