Enhancement of the Supercapacitive Performance of Cobalt-tin-cyanate Layered Structures through Conversion from 2D Materials to 1D Nanoﬁbers

: Rational design of the micro-nanomorphology is highly desired for metal hydroxides to achieve overall high-performance electrodes for supercapacitor and energy storage applications. Here, in the current study, we have succeeded in controlling the morphology of Sn/Co nanolayered structures to obtain plate and nanoﬁbrous morphologies. Additionally, the plate nanostructures could be transformed to obtain plate-nanoﬁbrous morphologies. In this trend, dual anions such as cyanate and nitrate are applied to intercalate among the nanolayers of cobalt-tin and act as building blocks or pillars, producing a series of nanolayered structures. By repulsion forces among the intercalated anions, the nanolayers of Sn/Co are curled and converted to nanoﬁbers. This conversion was conﬁrmed by scanning electron microscopy. In addition, the intercalation reactions and nanolayered structures were indicated by X-ray diffraction, thermal analyses and Fourier-transform infrared spectroscopy. The electrochemical supercapacitive behavior of the different nanostructures of Sn/Co HDS and Sn/Co LDH, such as plate, Plate-nanoﬁber and nanoﬁbrous morphology has been investigated in three assembly electrode system. The results suggested that the nanoﬁber morphology of Sn/Co LDH exhibited better speciﬁc capacitance performance than the other two morphologies. The enhanced speciﬁc capacitance (658 Fg − 1 ) and excellent cyclic stability (89%) of the nanoﬁbers of the Sn/Co LDH could be attributed to the synergistic effects between the electric double layer capacitive character of the tin and the pseudocapacitance nature of the cobalt.


Introduction
Various efforts have been undertaken to solve the energy issue, as the energy required in our daily lives is still totally dependent on fossil fuels, which causes environmental issues. Therefore, various types of the alternative energy windows have been explored in the search to develop an energy storage device which can provide enough power to fulfill our daily living requirements related to energy, as our most of human activities depend on energy. For this purpose, electrochemical abased energy conversion systems have received much attention, especially supercapacitors, which could provide a large amount of power density compared to batteries in short periods of time. Therefore, various efforts have been focused on developing efficient energy devices based on the supercapacitor [1][2][3][4][5]. There are four main parts in the capacitor, including the electrode, which is the most important part of the any energy device [6][7][8][9][10]. The electrode provides the device with the capability to store the charge and provide enough stability during the charge-discharge process. Various materials, such as carbon-based electrode materials, have been used to develop double layer-based supercapacitor devices, whereas metal oxide/hydroxide has been used to develop pseudocapacitive devices. Pseudocapacitive materials have been proven to be excellent specific capacitance materials, as their charge storing mechanisms are dependent on the oxidation and reduction processes over the electrode's surface [11,12]. Among all the transition metal oxides, cobalt-based oxide and hydroxide carbonates have received much attention owing to their sufficient electrical conductivity, easy preparation method, controllable morphology, and easy control of the interaction between positively and negatively charged layers during the layer metal hydroxides [1][2][3][4][5].
Layered metal hydroxides consist of a large and familiar group of inorganic compounds which have two branches; layered double hydroxides (LDHs) and hydroxyl double salt (HDS). Similar key structural features are observed for both LDHs and HDS. They consist of positively charged nanolayers and interlayered anions for charge balancing, but their nanolayers' compositions are different. LDHs contain a mixture of divalent and trivalent or tetravalent cations [13][14][15], while HDS have only divalent cations [16][17][18].
Recently, because of the high regulation of dominant compositions without the structure transformation of both LDHs and HDS, their wide applications were effective in the field of supercapacitors as battery-type materials. Transition metal carbonate hydroxides are considered promising scalable and effective alternatives with supercapacitive behaviors because of their ability to supply multiple redox activities and their relatively high electrical conductivity.
Though large theoretical specific capacitance values have been observed for the most metal hydroxides, their supercapacitances could be further improved by combining different metal cations into a host. In this trend, by incorporating various metal cations with the mono-metallic-based carbonate hydroxides, more redox reaction sites and higher electrical conductivity were observed for their composites. Thus, eventually, the electrochemical performance of these composites improved because of their synergistic effects [19,20]. For example, CoNiDH and Co 3 O 4 -CoNi-LDH are some of the most auspicious fictional materials for electrochemical applications such as electrocatalysis, Li-ion batteries and supercapacitors [19,20]. Apart from these, NiAl/LDH, MnCo/LDH and CoNi/LDH have widely studied with the aim of constructing efficient electrode materials for supercapacitance applications. Thus, double metal hydroxide materials are attracting increased attention in the field of supercapacitor electrode material research. However, their practical utilization is still limited by their relatively poor rate capability and cyclic retention [21]. In recent studies, they have demonstrated that micro-nano morphology and surface area are the key factors affecting the rate capability and long-term cyclic stability of the double metal hydroxide electrode material [22,23].
Thus, several studies are needed to explore the new micro-nanomorphology with large surface area for the double metal hydroxide to resolve the abovementioned issue. In this trend, the current study has tried to develop and enhance the performance of the cobalt supercapacitor electrode materials through designing nanofiber structures for layered metal double hydroxides with new species such as divalent and tetravalent tin. At the same time, it can provide data for the positive effect of the conversion of 2D nanomaterials to 1D nanofibers.
In the present work, a series of different nanostructures of the Sn/Co HDS and Sn/Co LDH materials, such as plate-nanofibers and nanofibrous morphologies have been synthesized by altering the percentage and the oxidation state of the precursor (Sn). The controlling of the morphology has been studied in detail through intercalating dual anions of both cyanate and nitrate anions in the confined space among the Sn/Co nanolayers. Then, the different morphologies leading to a different electrochemical property have been investigated. This study can provide a reference for future studies about morphological control and provide strategies to enhance the performance of supercapacitor electrode materials. Additionally, nanofibers may be useful for designing and fabricating nanodevices.
The first nanolayered structure was cobalt tin hydroxyl double salt (Sn/Co HDS). It consists of divalent cations of cobalt combined with divalent cations of tin. By using urea hydrolysis, cyanate anions were used as pillars to build nanolayered structures of hydroxyl double salts.
Typically, one liter of an aqueous solution of cobalt and tin was prepared through reacting 0.038 mol/L of cobalt nitrate [Co(NO 3 ) 2 ·6H 2 O] with 0.0095 mol/L of tin chloride (SnCl 2 ). The molar ratio of Co/Sn was 4. An appropriate amount of urea (0.5 mol/L) was added to the aqueous solution with vigorous stirring. The temperature reaction of the aqueous mixture was kept at 70 • C. The pH value of the reaction started to gradually increase. After 12 h, the pH reached 9 and the product was clear in the aqueous medium. After filtration and washing several times in deionized and distilled water, the product was dried under vacuum at room temperature. This sample was coded as CSHDS.
By changing divalent cations of tin to become tetravalent cations, another kind of nanolayered structure was produced. This second nanolayered structure was prepared through dissolving 0.0095 mol of tin tetrachloride (SnCl 4 ) instead of tin chloride (SnCl 2 ). Layered double hydroxides Sn/Co LDH was formed through a combination of tetravalent cations of Sn 4+ with divalent cations of Co 2+ . This sample was coded as CSLDH-1.
The third nanolayered structure was prepared through controlling the hydrolysis of urea by increasing the reaction temperature from 70 • C to 90 • C in addition to reducing the molar ratio of Co/Sn from 4 to 3 as seen in Table 1. This sample was coded as CSLDH-2.

Physical Characterization
The crystalline structures of the prepared materials were determined by X-ray diffraction (XRD) spectra which recorded on Rigaku, RINT 2200 Japan using CuKa (filtered) radiation (λ = 0.154 nm) between 1.8 and 50 degrees. The functional groups and interlayered anions were recorded through Fourier Transform Infrared Spectroscopy (FT-IR) over the wave number range 400-4000 cm −1 , using "Spectrum Two" from PerkinElmer Company. Thermal analyses (differential thermal analysis-DTA; differential thermal gravimetric-DTG; and thermal gravimetric analysis-TGA) of powdered samples up to 800 • C were carried out at a heating rate of 10 • C /min in flow of both nitrogen and air using a Seiko SSC 5200 Japan. The morphology, shape surface and distribution of the samples were directly obtained at room temperature using Scanning Electron Microscopy (SEM) JEOL:JSM-6330F, Tokyo, Japan.

Three Assembly Electrochemical Cell Setup and Electrode Preparation
The electrochemical performance of all the electrodes was examined in three electrode system with Pt sheet, Ag/AgCl electrode used as a reference and counter electrode, respectively. The working electrodes were fabricated using electrode material, activated carbon and PVDF at the mass ratio of 80:10:10 in NMP solvent. Afterward, slurry was coated on the washed Ni foam current collector with the effective area of 1 cm 2 and dried at 80 • C for 12 h. All electrochemical measurements were carried out in 2M KOH aqueous solution using CV and CD analysis.

Scanning Electron Microscopy
The prepared samples were coated with a thin film of platinum to increase the resolution of the images obtained through scanning electron microscopy (SEM). Figure 1 shows SEM images of CSHDS. It indicated that CSHDS has platelike morphology, agreeing with the literature on HDS [24,25]. The perpendicular orientations of the plates formed a porous structure, as shown in Figure 1a. The plates of the sample CSHDS were observed to have fine edges, indicating that it is in the nanoscale. Their plates' thickness is less than 100 nm, as shown in Figure 1c. The HDS structure was formed through decomposition of urea, as shown in the following equation: at 80 °C for 12 h. All electrochemical measurements were carried out in 2M KOH aqueous solution using CV and CD analysis.

Scanning Electron Microscopy
The prepared samples were coated with a thin film of platinum to increase the resolution of the images obtained through scanning electron microscopy (SEM). Figure 1 shows SEM images of CSHDS. It indicated that CSHDS has platelike morphology, agreeing with the literature on HDS [24,25]. The perpendicular orientations of the plates formed a porous structure, as shown in Figure 1a. The plates of the sample CSHDS were observed to have fine edges, indicating that it is in the nanoscale. Their plates' thickness is less than 100 nm, as shown in Figure 1c. The HDS structure was formed through decomposition of urea, as shown in the following equation: According to this equation, the concentration of cyanate gradually increased and the medium of the reaction converted to alkaline with high pH. These conditions are suitable for building a hydroxyl double salt structure. The presence of cyanate anions was confirmed by FT-IR results and EDS spectrum, which will be discussed below. In the case of CSLDH-1, nanofibers were observed as shown in Figure 2. Figure 2a,b reveal bundles of nanofibers. In addition, individual fibers with diameters of 50 nm are displayed in Figure 2c. However, the plate morphology is the most famous morphology for the natural samples of layered double hydroxides, which consist of di-and trivalent According to this equation, the concentration of cyanate gradually increased and the medium of the reaction converted to alkaline with high pH. These conditions are suitable for building a hydroxyl double salt structure. The presence of cyanate anions was confirmed by FT-IR results and EDS spectrum, which will be discussed below.
In the case of CSLDH-1, nanofibers were observed as shown in Figure 2. Figure 2a,b reveal bundles of nanofibers. In addition, individual fibers with diameters of 50 nm are displayed in Figure 2c. However, the plate morphology is the most famous morphology for the natural samples of layered double hydroxides, which consist of di-and trivalent cations [26]. Figure 2d confirms this speculation through displaying the conversion of Sn/Co plates to nanofibers. It shows that the major part of one plate has already transformed to nanofibers and the remaining part of the plate did not convert to nanofibers. cations [26]. Figure 2d confirms this speculation through displaying the conversion o Sn/Co plates to nanofibers. It shows that the major part of one plate has already trans formed to nanofibers and the remaining part of the plate did not convert to nanofibers. Energy dispersive X-ray spectrum analysis (EDS) of CSLDH-1 provides local infor mation of the concentrations of the different elements in the outermost layers of the nan ofibers. Cobalt and tin were observed in the EDS spectrum with similar percentages fo the starting salts. In addition, carbon, oxygen and nitrogen are clearly identified in th nanofibers, as shown in Figure 3. It means that EDS spectrum of CSLDH-1 confirmed th presence of cyanate anions as interlayered anions in addition to traces of nitrate anion because the ratio between carbon and nitrogen in the cyanate anions equal one. The nanofibrous morphology of the sample CSLDH-1 could be explained throug presence of tetravalent cations of Sn beside divalent cations of Co inside the nanolayer which created positive charges (+2). During the decomposition of urea, the concentratio of cyanate anions increased and the medium of the reaction became rich in cyanate anions Therefore, dual cyanate anions intercalated among the cationic layers through one side t neutralize the positive charges. The steric hindrance and repulsion between the bul Energy dispersive X-ray spectrum analysis (EDS) of CSLDH-1 provides local information of the concentrations of the different elements in the outermost layers of the nanofibers. Cobalt and tin were observed in the EDS spectrum with similar percentages for the starting salts. In addition, carbon, oxygen and nitrogen are clearly identified in the nanofibers, as shown in Figure 3. It means that EDS spectrum of CSLDH-1 confirmed the presence of cyanate anions as interlayered anions in addition to traces of nitrate anions because the ratio between carbon and nitrogen in the cyanate anions equal one.
cations [26]. Figure 2d confirms this speculation through displaying the conversion of Sn/Co plates to nanofibers. It shows that the major part of one plate has already transformed to nanofibers and the remaining part of the plate did not convert to nanofibers. Energy dispersive X-ray spectrum analysis (EDS) of CSLDH-1 provides local information of the concentrations of the different elements in the outermost layers of the nanofibers. Cobalt and tin were observed in the EDS spectrum with similar percentages for the starting salts. In addition, carbon, oxygen and nitrogen are clearly identified in the nanofibers, as shown in Figure 3. It means that EDS spectrum of CSLDH-1 confirmed the presence of cyanate anions as interlayered anions in addition to traces of nitrate anions because the ratio between carbon and nitrogen in the cyanate anions equal one. The nanofibrous morphology of the sample CSLDH-1 could be explained through presence of tetravalent cations of Sn beside divalent cations of Co inside the nanolayers which created positive charges (+2). During the decomposition of urea, the concentration of cyanate anions increased and the medium of the reaction became rich in cyanate anions. Therefore, dual cyanate anions intercalated among the cationic layers through one side to neutralize the positive charges. The steric hindrance and repulsion between the bulk The nanofibrous morphology of the sample CSLDH-1 could be explained through presence of tetravalent cations of Sn beside divalent cations of Co inside the nanolayers which created positive charges (+2). During the decomposition of urea, the concentration of cyanate anions increased and the medium of the reaction became rich in cyanate anions. Therefore, dual cyanate anions intercalated among the cationic layers through one side to neutralize the positive charges. The steric hindrance and repulsion between the bulk cyanate anions caused the distortion or curvature of the nanolayers of Sn/Co LDHs. This distortion or curvature led to the formation of nanofibers.
By increasing the content of tin in the sample CSLDH-2, the positive charges increased in the nanolayers and the amount of interlayered anions accordingly increased, causing more distortion and strong curvature for the layers and producing clear nanofibers because of the repulsion forces among the dual anions. Figure 4 shows that the sample CSLDH-2 has clear nanofibers, confirming this speculation. The diameter of these nanofibers was less than 100 nm, as shown in Figure 4b,c. cyanate anions caused the distortion or curvature of the nanolayers of Sn/Co LDHs. This distortion or curvature led to the formation of nanofibers. By increasing the content of tin in the sample CSLDH-2, the positive charges increased in the nanolayers and the amount of interlayered anions accordingly increased, causing more distortion and strong curvature for the layers and producing clear nanofibers because of the repulsion forces among the dual anions. Figure 4 shows that the sample CSLDH-2 has clear nanofibers, confirming this speculation. The diameter of these nanofibers was less than 100 nm, as shown in Figure 4b,c.

Powder X-ray Diffraction
X-ray Diffraction (XRD) was used to analyze the phase composition and crystal structure of the prepared materials. Figure 5a shows the XRD pattern of the sample CSHDS. The XRD pattern of CSHDS is typical of layered materials, showing sharp symmetric reflections at a low angle with interlayered spacing (0.78 nm) and weak asymmetric reflections at high angles with interlayered spacing (0.39 nm and 0.268 nm). The good agreement between these values corresponding to successive diffractions by planes, i.e., 0.78

Powder X-ray Diffraction
X-ray Diffraction (XRD) was used to analyze the phase composition and crystal structure of the prepared materials. Figure 5a shows the XRD pattern of the sample CSHDS. The XRD pattern of CSHDS is typical of layered materials, showing sharp symmetric reflections at a low angle with interlayered spacing (0.78 nm) and weak asymmetric reflections at high angles with interlayered spacing (0.39 nm and 0.268 nm). The good agreement between these values corresponding to successive diffractions by planes, i.e., 0.78 nm = 2 × 0.39 nm = 3 × 0.268 nm, reveals nanolayered structures with highly packed stacks of HDS layers. Although there are no XRD results reported in the literature for cobalt-tin-cyanate HDS, these diffraction peaks are in agreement with the cobalt nickel carbonate hydroxide hydrate phase found using JCPDS card number 40-216. For nanolayered hydroxyl double salt structures, the main peaks observed at 0.78 nm, 0.39 nm, and 0.268 nm, which are agreement with the diffraction of the basal planes-(003), (006), and (009), respectively. In addition, the non-basal reflection at 0.299 nm was considered to be relative to the (100) plane. The value for the (003) peak at 0.78 nm is slightly larger than the value reported for cobalt nickel hydroxyl double salt, whose value is 0.76 nm in the case of the carbonate anion as the guest and the cobalt combined with nickel [20,27]. This value depends on the size of the anion. This shift from 0.76 nm to 0.78 nm suggests the presence of cyanate or nitrate anions instead of carbonate in addition to the incorporation of tin instead of nickel in the lattice of hydroxyl double salts [28,29].  (009), respectively. In addition, the non-basal reflection at 0.299 nm was considered to be relative to the (100) plane. The value for the (003) peak at 0.78 nm is slightly larger than the value reported for cobalt nickel hydroxyl double salt, whose value is 0.76 nm in the case of the carbonate anion as the guest and the cobalt combined with nickel [20,27]. This value depends on the size of the anion. This shift from 0.76 nm to 0.78 nm suggests the presence of cyanate or nitrate anions instead of carbonate in addition to the incorporation of tin instead of nickel in the lattice of hydroxyl double salts [28,29]. By changing tin from a divalent element to tetravalent element, different kind of layered structures were observed, as shown in Figure 5b. The XRD pattern of the sample CSLDH-1 showed three peaks at spacing 0.794 nm, 0.393 nm, and 0.269 nm. This pattern showed strong and sharp peaks at low 2Ѳ and weak peaks at high 2Ѳ, indicating some common features of the layered structures. For layered double hydroxides (LDHs), hydrotalcitelike materials, the reflections of the main planes (003), (006), and (009) agree with the observed peaks at spacing 0.794 nm, 0.393 nm, and 0.269 nm, respectively. However, the value of the reflection of the main plane (003) which was observed at 0.79 nm, is significantly larger than the value reported for natural hydrotalcite, whose value is 0.76 nm in the case of the carbonate anion as the guest [30,31]. This value depends on the size and the orientation of the anion in addition to the thickness of the brucitelike layers (0.48 nm for hydrotalcite). This means that the interlayered spacing is not compatible with the size of carbonate anion suggesting presence of cyanate or nitrate anions.
In case of the sample CSLDH-2, the main peaks of the layered structure became opaque. Figure 5c shows that CSLDH-2 has a non-crystalline structure because of the high content of tetravalent tin, leading to presence of high positive charges inside the nanolayers of the LDHs. It means that the high positive charges caused high concentrations of anions among the nanolayers, leading to high distortion and more curvature for the By changing tin from a divalent element to tetravalent element, different kind of layered structures were observed, as shown in Figure 5b. The XRD pattern of the sample CSLDH-1 showed three peaks at spacing 0.794 nm, 0.393 nm, and 0.269 nm. This pattern showed strong and sharp peaks at low 2  (009), respectively. In addition, the non-basal reflection at 0.299 nm was considered to be relative to the (100) plane. The value for the (003) peak at 0.78 nm is slightly larger than the value reported for cobalt nickel hydroxyl double salt, whose value is 0.76 nm in the case of the carbonate anion as the guest and the cobalt combined with nickel [20,27]. This value depends on the size of the anion. This shift from 0.76 nm to 0.78 nm suggests the presence of cyanate or nitrate anions instead of carbonate in addition to the incorporation of tin instead of nickel in the lattice of hydroxyl double salts [28,29]. By changing tin from a divalent element to tetravalent element, different kind of layered structures were observed, as shown in Figure 5b. The XRD pattern of the sample CSLDH-1 showed three peaks at spacing 0.794 nm, 0.393 nm, and 0.269 nm. This pattern showed strong and sharp peaks at low 2Ѳ and weak peaks at high 2Ѳ, indicating some common features of the layered structures. For layered double hydroxides (LDHs), hydrotalcitelike materials, the reflections of the main planes (003), (006), and (009) agree with the observed peaks at spacing 0.794 nm, 0.393 nm, and 0.269 nm, respectively. However, the value of the reflection of the main plane (003) which was observed at 0.79 nm, is significantly larger than the value reported for natural hydrotalcite, whose value is 0.76 nm in the case of the carbonate anion as the guest [30,31]. This value depends on the size and the orientation of the anion in addition to the thickness of the brucitelike layers (0.48 nm for hydrotalcite). This means that the interlayered spacing is not compatible with the size of carbonate anion suggesting presence of cyanate or nitrate anions.
In case of the sample CSLDH-2, the main peaks of the layered structure became opaque. Figure 5c shows that CSLDH-2 has a non-crystalline structure because of the high content of tetravalent tin, leading to presence of high positive charges inside the nanolayers of the LDHs. It means that the high positive charges caused high concentrations of anions among the nanolayers, leading to high distortion and more curvature for the and weak peaks at high 2 Appl. Sci. 2021, 11, x FOR PEER REVIEW nm = 2 × 0.39 nm = 3 × 0.268 nm, reveals nanolayered structures with h of HDS layers. Although there are no XRD results reported in the liter cyanate HDS, these diffraction peaks are in agreement with the cob hydroxide hydrate phase found using JCPDS card number 40-216. F droxyl double salt structures, the main peaks observed at 0.78 nm, 0.3 which are agreement with the diffraction of the basal planes-(003), spectively. In addition, the non-basal reflection at 0.299 nm was cons to the (100) plane. The value for the (003) peak at 0.78 nm is slightly l reported for cobalt nickel hydroxyl double salt, whose value is 0.76 n carbonate anion as the guest and the cobalt combined with nickel [20 pends on the size of the anion. This shift from 0.76 nm to 0.78 nm su of cyanate or nitrate anions instead of carbonate in addition to the instead of nickel in the lattice of hydroxyl double salts [28,29]. By changing tin from a divalent element to tetravalent element, d ered structures were observed, as shown in Figure 5b. The XRD pa CSLDH-1 showed three peaks at spacing 0.794 nm, 0.393 nm, and 0.2 showed strong and sharp peaks at low 2Ѳ and weak peaks at high common features of the layered structures. For layered double hydr drotalcitelike materials, the reflections of the main planes (003), (006), the observed peaks at spacing 0.794 nm, 0.393 nm, and 0.269 nm, res the value of the reflection of the main plane (003) which was observe nificantly larger than the value reported for natural hydrotalcite, wh in the case of the carbonate anion as the guest [30,31]. This value depe the orientation of the anion in addition to the thickness of the brucite for hydrotalcite). This means that the interlayered spacing is not com of carbonate anion suggesting presence of cyanate or nitrate anions.
In case of the sample CSLDH-2, the main peaks of the layere opaque. Figure 5c shows that CSLDH-2 has a non-crystalline structure content of tetravalent tin, leading to presence of high positive charges ers of the LDHs. It means that the high positive charges caused hig anions among the nanolayers, leading to high distortion and mor , indicating some common features of the layered structures. For layered double hydroxides (LDHs), hydrotalcitelike materials, the reflections of the main planes (003), (006), and (009) agree with the observed peaks at spacing 0.794 nm, 0.393 nm, and 0.269 nm, respectively. However, the value of the reflection of the main plane (003) which was observed at 0.79 nm, is significantly larger than the value reported for natural hydrotalcite, whose value is 0.76 nm in the case of the carbonate anion as the guest [30,31]. This value depends on the size and the orientation of the anion in addition to the thickness of the brucitelike layers (0.48 nm for hydrotalcite). This means that the interlayered spacing is not compatible with the size of carbonate anion suggesting presence of cyanate or nitrate anions.
In case of the sample CSLDH-2, the main peaks of the layered structure became opaque. Figure 5c shows that CSLDH-2 has a non-crystalline structure because of the high content of tetravalent tin, leading to presence of high positive charges inside the nanolayers of the LDHs. It means that the high positive charges caused high concentrations of anions among the nanolayers, leading to high distortion and more curvature for the nanolayers of LDHs. Therefore, the peaks of the XRD became opaque and the nanofibers became clearer in SEM images, which was discussed above. However, the weak peak observed at spacing 0.798 nm indicates presence of layered double hydroxide in a distortion state.
According to the SEM images and X-ray results, the transformation of nanolayered materials to nanofibers can be explained through schematic representation in Figure 6. From the known layer thickness, 0.48 nm, and the size of cyanate anion, 0.34 nm, the interlayer spacing available for the anion was calculated as 0.31 nm. It was considered that the cyanate anions have bulk groups having high electron density (e.g., cyanide group with triple bond). Additionally, the size of the nitrate molecules is 0.28 nm having high electron density. The intercalation of the dual molecules of cyanate anions or nitrate anion among the nanolayers to neutralize the positive charges causes steric hindrance for the nanolayers. Therefore, the repulsion forces among the cyanide groups or nitrate groups led to the nanolayers curling, thereby converting the nanolayers to nanofibers, as shown in Figure 6.
nanolayers of LDHs. Therefore, the peaks of the XRD became opaque and the nan became clearer in SEM images, which was discussed above. However, the weak p served at spacing 0.798 nm indicates presence of layered double hydroxide in a dis state.
According to the SEM images and X-ray results, the transformation of nano materials to nanofibers can be explained through schematic representation in Fi From the known layer thickness, 0.48 nm, and the size of cyanate anion, 0.34 nm, terlayer spacing available for the anion was calculated as 0.31 nm. It was consider the cyanate anions have bulk groups having high electron density (e.g., cyanide with triple bond). Additionally, the size of the nitrate molecules is 0.28 nm havin electron density. The intercalation of the dual molecules of cyanate anions or nitrat among the nanolayers to neutralize the positive charges causes steric hindrance nanolayers. Therefore, the repulsion forces among the cyanide groups or nitrate led to the nanolayers curling, thereby converting the nanolayers to nanofibers, as in Figure 6.

Fourier-Transform Infrared Spectroscopy
The nature and symmetry of functional groups of CSHDS, CSLDH-1 and CS have been identified by the FT-IR technique, as shown in Figure 7.

Fourier-Transform Infrared Spectroscopy
The nature and symmetry of functional groups of CSHDS, CSLDH-1 and CSLDH-2 have been identified by the FT-IR technique, as shown in Figure 7. Figure 7a shows the spectrum of CSHDS. The interlayered anions of CSHDS were confirmed by the appearance of a clear band at 2206 cm -1 corresponding to the vibrational mode of cyanate (N≡C-O − ).
Small two bands were observed at 1388 cm −1 and 1461 cm −1 , indicating that small amounts of nitrate anions were intercalated among the nanolayers [31,32]. Hydroxyl groups of CSHDS were also detected by a broad band at 3423 cm −1 . This broadness is due to the hydrogen bonds of the hydroxyl groups. These hydrogen bonds were confirmed by the sharp and strong bands around 2923 cm -1 because the molecules of the interlayered water which hydrogen-bonded to the interlayered anions caused the stretching mode for the O-H bands [33]. Additionally, the water molecules exhibited the bending mode band close to 1637 cm −1 [28,32]. Small two bands were observed at 1388 cm −1 and 1461 cm −1 , indicating that small amounts of nitrate anions were intercalated among the nanolayers [31,32]. Hydroxyl groups of CSHDS were also detected by a broad band at 3423 cm −1 . This broadness is due to the hydrogen bonds of the hydroxyl groups. These hydrogen bonds were confirmed by the sharp and strong bands around 2923 cm -1 because the molecules of the interlayered water which hydrogen-bonded to the interlayered anions caused the stretching mode for the O-H bands [33]. Additionally, the water molecules exhibited the bending mode band close to 1637 cm −1 [28,32].
In the case of CSLDH-1, Figure 7b shows a strong band at 2217 cm −1 , which was formed due to symmetrical vibration ν1 of NCO. Additionally, the clear peak observed at 634 cm −1 could be attributed to the ν2 form of cyanate ion. An important phenomenon is observed for the existence of NCO ions inside the interlayers beside OH groups [33]. It revealed that there is a strong effect of the electron density of NCO on the vibration of the OH groups. The broad OH vibration band which resolved into two bands was ascribed to the existence of the NCO group beside the OH groups. The unaffected OH groups showed an absorption band at 3629 cm −1 , as reported for the usual hydroxyl groups. Additionally, there is another band which was observed at a lower value of 3467 cm −1 . The shifting of the band of the hydroxyl group was due to the lowering of the O-H bond electron density because of the effect of the cyanide group. This phenomenon is in agreement with the results of Xu et al. [34] that indicated the outcome of the existence of nitrate ions on the bands of LDH. The shoulder peaks recorded at 2925 cm −1 indicate the stretching OH bonds that are due to the interlayer water molecules and/or produced from the hydrogen bonds formed with cyanate ions [15,26,35,36]. The peak at 1617 cm −1 was due to the bending band of the water molecules [37]. Additionally, the weak peaks observed at both 1457 cm −1 and 1384 cm −1 indicated that there are traces of nitrate as secondary anions. Figure 7c showed that the sample CSLDH-2 has the main bands of LDH's structure in the case where the guests are nitrate anion. Clear bands for nitrate anions were observed at 1384 cm −1 and 1457 cm −1 . Additionally, the hydroxyl band and water band were observed at 3434 cm −1 and 1637 cm −1 . The hydrogen bonds were confirmed by strong bands at 2923 cm −1 and 2852 cm −1 , indicating that the nitrate anions bonded with hydroxyl groups through H-bonds. In the case of CSLDH-1, Figure 7b shows a strong band at 2217 cm −1 , which was formed due to symmetrical vibration ν 1 of NCO. Additionally, the clear peak observed at 634 cm −1 could be attributed to the ν 2 form of cyanate ion. An important phenomenon is observed for the existence of NCO ions inside the interlayers beside OH groups [33]. It revealed that there is a strong effect of the electron density of NCO on the vibration of the OH groups. The broad OH vibration band which resolved into two bands was ascribed to the existence of the NCO group beside the OH groups. The unaffected OH groups showed an absorption band at 3629 cm −1 , as reported for the usual hydroxyl groups. Additionally, there is another band which was observed at a lower value of 3467 cm −1 . The shifting of the band of the hydroxyl group was due to the lowering of the O-H bond electron density because of the effect of the cyanide group. This phenomenon is in agreement with the results of Xu et al. [34] that indicated the outcome of the existence of nitrate ions on the bands of LDH. The shoulder peaks recorded at 2925 cm −1 indicate the stretching OH bonds that are due to the interlayer water molecules and/or produced from the hydrogen bonds formed with cyanate ions [15,26,35,36]. The peak at 1617 cm −1 was due to the bending band of the water molecules [37]. Additionally, the weak peaks observed at both 1457 cm −1 and 1384 cm −1 indicated that there are traces of nitrate as secondary anions. Figure 7c showed that the sample CSLDH-2 has the main bands of LDH's structure in the case where the guests are nitrate anion. Clear bands for nitrate anions were observed at 1384 cm −1 and 1457 cm −1 . Additionally, the hydroxyl band and water band were observed at 3434 cm −1 and 1637 cm −1 . The hydrogen bonds were confirmed by strong bands at 2923 cm −1 and 2852 cm −1 , indicating that the nitrate anions bonded with hydroxyl groups through H-bonds.

Thermal Analyses
The thermal analyses (differential thermal analysis-DTA; differential thermal gravimetric-DTG; and thermal gravimetric analysis-TGA) of the prepared materials were measured in the presence of both nitrogen gas and air to indicate the oxidation reactions of the divalent cations (cobalt and tin) and the cyanate anions. Figure 8a shows the thermal analyses of CSHDS in the presence of nitrogen. The TGA curve shows the total weight loss that occurred throughout the two stages. measured in the presence of both nitrogen gas and air to indicate the oxidation reactio of the divalent cations (cobalt and tin) and the cyanate anions. Figure 8a shows the therm analyses of CSHDS in the presence of nitrogen. The TGA curve shows the total wei loss that occurred throughout the two stages. In the first stage, the water was lost through three steps [38]. It was found that wt.%, 7 wt.% and 8.3 wt.% were lost at 107 °C, 150 °C and 191 °C, respectively. Th losses were confirmed by DTG and DTA. DTA showed two endothermic peaks at 70 and 133 °C. It means that the water molecules are bonded in the lattice by two differ species-nitrate and cyanate anions [14,15]. In the second stage, 11.7 wt.% was lost, in cating the removal of the interlayered anions at 281 °C. The thermal decomposition of interlayered anions was confirmed by two endothermic peaks at 218 °C and 265 °C in DTA curve. It means that there are two anions in the lattice of CSHDS.
By measuring the thermal analyses in presence of oxygen, Figure 8b showed a stro exothermic peak in DTA curve of CSHDS indicating oxidation reactions of cobalt and in addition to cyanate anions at 233 °C. In addition, the two endothermic peaks of wa removal were also observed at 74 °C and 140 °C. The TGA and DTG curves in presence oxygen showed similar diagrams to that in nitrogen gas, confirming the presence of t anions and intercalated water in the lattice of CSHDS.
The thermal characteristics of the second sample, CSLDH-1 in nitrogen gas, were termined by DTA, DTG and TGA, as shown in Figure 9a. The total weight loss occurr through four steps, indicating removal of surface water, interlayered water, cyanate a ons and nitrate anions, respectively [14,15]. The DTG curve showed clear two peaks the removal of the interlayered anions. Additionally, DTA revealed two endotherm peaks at 250.6 °C and 307.9 °C, confirming the presence of two interlayered anions, c nate and nitrate, agreeing with the FTIR data. In the first stage, the water was lost through three steps [38]. It was found that 4.6 wt.%, 7 wt.% and 8.3 wt.% were lost at 107 • C, 150 • C and 191 • C, respectively. These losses were confirmed by DTG and DTA. DTA showed two endothermic peaks at 70 • C and 133 • C. It means that the water molecules are bonded in the lattice by two different species-nitrate and cyanate anions [14,15]. In the second stage, 11.7 wt.% was lost, indicating the removal of the interlayered anions at 281 • C. The thermal decomposition of the interlayered anions was confirmed by two endothermic peaks at 218 • C and 265 • C in the DTA curve. It means that there are two anions in the lattice of CSHDS.
By measuring the thermal analyses in presence of oxygen, Figure 8b showed a strong exothermic peak in DTA curve of CSHDS indicating oxidation reactions of cobalt and tin in addition to cyanate anions at 233 • C. In addition, the two endothermic peaks of water removal were also observed at 74 • C and 140 • C. The TGA and DTG curves in presence of oxygen showed similar diagrams to that in nitrogen gas, confirming the presence of two anions and intercalated water in the lattice of CSHDS.
The thermal characteristics of the second sample, CSLDH-1 in nitrogen gas, were determined by DTA, DTG and TGA, as shown in Figure 9a. The total weight loss occurred through four steps, indicating removal of surface water, interlayered water, cyanate anions and nitrate anions, respectively [14,15]. The DTG curve showed clear two peaks for the removal of the interlayered anions. Additionally, DTA revealed two endothermic peaks at 250.6 • C and 307.9 • C, confirming the presence of two interlayered anions, cyanate and nitrate, agreeing with the FTIR data.
The different thermal processes of the sample CSLDH-1 are clearly distinguished when its thermal analyses are carried out in presence of air, as shown in Figure 9b. Figure 9b shows that TGA curve of CSLDH-1 has five weight losses with the different slopes indicating the removal of surface water, the removal of interlayered water, the oxidation of cyanate, the oxidation of nitrate and the dehydroxylation process. The DTG curve indicated the oxidation of both cyanate and nitrate anions through two peaks at 231 • C and 257 • C, respectively. Additionally, the oxidation reactions were confirmed by a strong exothermic peak at 236 • C in addition to weak peak at 270 • C. The different thermal processes of the sample CSLDH-1 are clearly distinguis when its thermal analyses are carried out in presence of air, as shown in Figure 9b. Fig  9b shows that TGA curve of CSLDH-1 has five weight losses with the different slo indicating the removal of surface water, the removal of interlayered water, the oxidat of cyanate, the oxidation of nitrate and the dehydroxylation process. The DTG curve in cated the oxidation of both cyanate and nitrate anions through two peaks at 231 °C 257 °C, respectively. Additionally, the oxidation reactions were confirmed by a strong othermic peak at 236 °C in addition to weak peak at 270 °C.
In the case of CSLDH-2, Figure 10a shows the thermal analyses in the presenc nitrogen gas. Three weight losses were observed in the TGA curve, indicating the ex ence of one kind of the interlayered anions agreeing with FTIR data. Figure 10a sho that 9 wt.% of surface water was lost at 99°C and 6.2 wt.% of the interlayered water w removed at 231 °C [39]. In addition, 5.2 wt.% of nitrate anions were lost at 321 °C. D and DTA confirmed the presence of one kind of anions through one peak at 263 °C 269 °C, respectively. In presence of air, these three weight losses were clearly observed Figure 10b through TG and DTG diagrams. These peaks were confirmed by three en thermic peaks in DTA curve at 57 °C, 165 °C and 247 °C. In the case of CSLDH-2, Figure 10a shows the thermal analyses in the presence of nitrogen gas. Three weight losses were observed in the TGA curve, indicating the existence of one kind of the interlayered anions agreeing with FTIR data. Figure 10a shows that 9 wt.% of surface water was lost at 99 • C and 6.2 wt.% of the interlayered water was removed at 231 • C [39]. In addition, 5.2 wt.% of nitrate anions were lost at 321 • C. DTG and DTA confirmed the presence of one kind of anions through one peak at 263 • C and 269 • C, respectively. In presence of air, these three weight losses were clearly observed in Figure 10b through TG and DTG diagrams. These peaks were confirmed by three endothermic peaks in DTA curve at 57 • C, 165 • C and 247 • C. The different thermal processes of the sample CSLDH-1 are clearly distinguish when its thermal analyses are carried out in presence of air, as shown in Figure 9b. Fig  9b shows that TGA curve of CSLDH-1 has five weight losses with the different slo indicating the removal of surface water, the removal of interlayered water, the oxidat of cyanate, the oxidation of nitrate and the dehydroxylation process. The DTG curve in cated the oxidation of both cyanate and nitrate anions through two peaks at 231 °C a 257 °C, respectively. Additionally, the oxidation reactions were confirmed by a strong othermic peak at 236 °C in addition to weak peak at 270 °C.
In the case of CSLDH-2, Figure 10a shows the thermal analyses in the presence nitrogen gas. Three weight losses were observed in the TGA curve, indicating the ex ence of one kind of the interlayered anions agreeing with FTIR data. Figure 10a sho that 9 wt.% of surface water was lost at 99°C and 6.2 wt.% of the interlayered water w removed at 231 °C [39]. In addition, 5.2 wt.% of nitrate anions were lost at 321 °C. D and DTA confirmed the presence of one kind of anions through one peak at 263 °C a 269 °C, respectively. In presence of air, these three weight losses were clearly observed Figure 10b through TG and DTG diagrams. These peaks were confirmed by three en thermic peaks in DTA curve at 57 °C, 165 °C and 247 °C.

Electrochemical Performance of CSLDH Electrode
The electrochemical performance is strongly known to depend on the apparent morphology and structure of the material. The microstructure (nanostructured) of the surface of the electrode delivers a high surface area to the electrode materials, which are advantageous for the higher intercalation phenomena of the electric charges and hence, improved the performance owing to the high exchange of ions in electrode materials. The amount/percentage and oxidation state of the precursor alters the surface morphology, and these morphology changes affect the electrochemical properties of the electrode materials. Therefore, to understand the morphological effect of fabricated Sn/Co HDS and Sn/Co LDHs on the electrochemical response and to find out the optimized high performance condition for the electrode preparation in present study, we carried out cyclic voltammetry (CV) and galvanostatic charge-discharge (CD) measurement investigation in a three electrode system (Figures 11 and 12). These measurements are the most prominent tools for assessing the capacitive behavior of the electrodes. All the measurements were performed in a 2M KOH electrolytic solution.
. Sci. 2021, 11, x FOR PEER REVIEW 13 of With the increasing scan rate, the CSLDH-2 electrode seems to have improved terms of holding the nature of its CV profile compared to the other electrodes, proposi that the rate capability of this electrode is significantly higher. On the other hand, a partial contribution from the double layer mechanism is a observed, as evidenced by the small rectangular area that appeared between −0.05 to V. Similar to oxide-based electrodes, the capacitance of these electrodes is thought to occ predominantly because of pseudocapacitance mechanism that belongs to the reversib redox mechanism occurring between the electrode and the electrolyte.
In conclusion, the CV curves of all the electrodes show that the current of the red Once the CV analysis was performed to verify the capacity nature, including pse docapacitance, the galvanostatic charge-discharge measurement was carried out to inv tigate the charge-discharge performance for all prepared electrodes. For the better a plicability of the electrodes, it can be directly evaluated by the charge-discharge perf mance. Figure 12a shows the CD curves of the CSHDS, CSLDH-1 and CSLDH-2 at the cu rent density of the 1 Ag −1 in potential range of the 0.0 to 0.5 V. Consistent with the outcom of the CV analysis of these three electrodes, the discharge period of the CSHDS electro is significantly higher than that of the CSLDH-1 electrode, which has plate morpholog Furthermore, the discharge time considerably increased when the plate morphology co pletely transformed into a one dimensional morphology. Such enhanced performance the electrochemical response might be due to high surface-to-volume ratio and elect conductivity, which allows more redox reactions to occur and hence better capacity to achieved. All the electrodes indicated an analogous behavior over the course of bo charge and discharge process. Contrasting with the linear charge-discharge curves wh are characteristics of EDLC, the prominent plateau was observed in the discharge curv which confirmed the faradic reaction for all three electrodes that again confirms that t capacitance is achieved predominantly from the faradic reaction mechanism and thus in good agreement with CV observation. To further examine the electrochemical behavi In this regard, the initial behavior (faradic or non-faradic reaction) and specific capacitance of the electrodes were examined by the CV analysis in the suitable potential range of 0.0-0.55 V with numerous scan rates from 5 to 80 mVs −1 . For the comparative assessment of the CV analysis results, the CSHDS, CSLDH-1 and CSLDH-2 electrodes performed at fixed potential scan rate (10 mVs −1 ) in the potential range of 0.0 to 0.55 V are shown in Figure 11a. The CV profiles of the CSHDS, CSLDH-1 and CSLDH-2 electrodes show distinct from each other in terms of oxidation (cathodic sweep; positive current) and reduction peaks (anodic sweeps; positive current) during the charging and discharging cycle. All the electrodes revealed the predominant, distinct pair of redox peaks which indicate that the charge storage was majorly from the faradaic pseudocapacitance rather than from the electrochemical double layer capacitor. Specific capacitance is an important parameter for evaluating performance due to its direct link with the energy storage of the pseudocapacitor, which is generally denoted by E=1/2 CV 2 . Additionally, it is well known that the charges stored change with respect to the area under the CV curves, which are directly proportional to the specific capacitance. It can be found that the integrated area under the CV of CSLDH-2 was larger than that of the CSLDH-1 and CSHDS electrodes, indicating the higher specific capacitance provided by the CSLDH-2 electrode. This enhanced performance of the CSLDH-2 electrode was attributed to synergistic effects between the electric double layer capacitive character of the tin and the pseudocapacitance nature of the cobalt and also indicated that the CSHDS and CSLDH-1 electrodes have poor rate performance because of slow charge diffusion rate. Secondly, transformations in nanosize and fibrous morphology provide a larger surface area to volume ratio and better pore size in comparison to the CSLDH-1 and CSHDS electrodes, and have strong effects on the enhanced performance of CSLDH-2 because they can expose more active sites for the intercalation of the ions during electrochemical analysis.
Furthermore, the capacity behavior of the CSHDS, CSLDH-1 and CSLDH-2 electrodes was studied by CV analysis at different voltage scan rates (10-80 mVs −1 ), as demonstrated in Figure 11. The individual CV profiles displayed clear pairs of oxidation and reduction peaks. In Figure 11b, a pair of redox peaks are observed for the CSHDS electrode with platelike morphology at a scan rate of 5 mVs −1 , which are assigned to the reversible redox reactions of Sn 2+ /Sn 4+ and Co 2+ /Co 3+ transitions associated with OH anions. At a high scan rate of 80 mVs −1 , the anodic and cathodic peaks altered, which suggests that this redox reaction was easily reversible and could be used for fast charging/discharging in supercapacitors. An almost similar observation was also found in the CSLDH-1 electrode, which has a dominantly fibrous morphology. Furthermore, the optimized electrode of CSLDH-2, which has one dimensional nanofibrous morphology, shows a predominant redox reaction during anodic and cathodic sweeps in CV.
With the increasing scan rate, the CSLDH-2 electrode seems to have improved in terms of holding the nature of its CV profile compared to the other electrodes, proposing that the rate capability of this electrode is significantly higher.
On the other hand, a partial contribution from the double layer mechanism is also observed, as evidenced by the small rectangular area that appeared between −0.05 to 0.1 V. Similar to oxide-based electrodes, the capacitance of these electrodes is thought to occur predominantly because of pseudocapacitance mechanism that belongs to the reversible redox mechanism occurring between the electrode and the electrolyte.
In conclusion, the CV curves of all the electrodes show that the current of the redox peak increases with increasing scan rate. Moreover, from the CV curves, it is observable that the oxidation-reduction peaks are moving towards the higher and lower potentials due to the reinforced electric polarization and feasible kinetic irreversibility of the electrolytic ion on the electrode surface [40]. The potential of the electrodes changes more and more, leading to inadequate redox reactions on the interfaces between the electrode and the electrolyte. Therefore, the pseudocapacitance primarily derived from redox reactions slowly reduces. The material exhibited redox peak in CV curve should not be considered a pseudocapacitor, as the capacitance of the electrode keeps altering over the whole potential window. Therefore, the electrochemical performance of the Sn/Co electrodes was measured in terms of the specific capacity instead of specific capacitance [40].
Once the CV analysis was performed to verify the capacity nature, including pseudocapacitance, the galvanostatic charge-discharge measurement was carried out to investigate the charge-discharge performance for all prepared electrodes. For the better applicability of the electrodes, it can be directly evaluated by the charge-discharge performance. Figure 12a shows the CD curves of the CSHDS, CSLDH-1 and CSLDH-2 at the current density of the 1 Ag −1 in potential range of the 0.0 to 0.5 V. Consistent with the outcomes of the CV analysis of these three electrodes, the discharge period of the CSHDS electrode is significantly higher than that of the CSLDH-1 electrode, which has plate morphology. Furthermore, the discharge time considerably increased when the plate morphology completely transformed into a one dimensional morphology. Such enhanced performance in the electrochemical response might be due to high surface-to-volume ratio and electric conductivity, which allows more redox reactions to occur and hence better capacity to be achieved. All the electrodes indicated an analogous behavior over the course of both charge and discharge process. Contrasting with the linear charge-discharge curves which are characteristics of EDLC, the prominent plateau was observed in the discharge curves, which confirmed the faradic reaction for all three electrodes that again confirms that the capacitance is achieved predominantly from the faradic reaction mechanism and thus is in good agreement with CV observation. To further examine the electrochemical behavior, the charge-discharge analysis was performed at various current densities from 1-7 Ag −1 . All the electrodes show a semi-symmetric CD curve which demonstrates rapid response and excellent electrochemical reversibility and confirms the faradic behavior of the electrodes [41,42]. The CSLDH-2 electrode shows higher CD time over the entire range of current density as compared to the other two electrodes. These findings are well matched with the results from the CV analysis. The obtained charge-discharge results were further applied to determine the specific capacitance values using following equation: where C is the specific capacitance, I is stand for the discharge current density, ∆t is the charge-discharge time, ∆V is the working potential window, and w is the mass of active material which present on the current collector.
The calculated specific capacitance of the CSLDH-2 electrode is 658 Fg −1 at current density of 1 Ag −1 which is higher than CSHDS (520 Fg −1 ) and CSLDH-1 (434 Fg −1 ) electrodes. The higher specific capacitance of the CSLDH-2 electrode is due to the nanosize of the fibrous morphology. Figure 12d represents the CD curves of the CSLDH-2 electrode, whereas Figures 12c and 11b show the CD curves of the CSLDH-1 and CSHDS electrodes, respectively, at current densities ranging from 1 Ag −1 to 7 Ag −1 . The calculated specific capacitance of the CSLDH-1 and CSHDS electrodes at different current densities of 1, 2, 3, 4, 5 and 7 Ag −1 were 658, 584, 330, 312, 290, 280 Fg −1 , respectively. For the CSLDH-1 electrode, the estimated specific capacitances were 520, 444, 300, 176, 120, 98 Fg −1 . Similarly, the specific capacitances of CSHDS electrode were 434, 312, 210, 96, 57, 42 Fg −1 , respectively. Among all three of the electrodes, CSLDH-2 electrode exhibited higher specific capacitance because of its nanofibrous morphology, which provides higher surface area and more active sites for the electrolyte intercalation-deintercalation during the CD process and maximizes the utilization of the CSLDH-2 electrode. Figure 13a represents the specific capacitance of the CSHDS, CSLDH-1 and CSLDH-2 at different current densities. From Figure 13a, it is clearly demonstrated that with an increase in the current densities, the specific capacitance decreased for all three electrodes. The highest specific capacitance (e.g., 658 Fg −1 at 1 Ag −1 current density) was observed in the complete range of current density with an electrode prepared by an optimal percentage/quantity of the precursor, which is a CSLDH-2 electrode. Moreover, the specific capacitance slowly decreased with an increase in the operating current density, and then demonstrated steeper drops including the other two electrodes. This is due to low intercalation of the electrolyte ions into the bulk of the electrode, which then does not have much time to take a part in the reaction with the electrolyte at a higher current density. The specific capacitance of the nanofibrous CSLDH-2 electrode is higher than the previously reported cobalt-tin composite electrodes. For example, nanoparticle of CoSn(OH) 6 showed higher specific capacitance of 450 Fg −1 , and the SnO 2 /Co 3 O 4 -C composite exhibited higher specific capacitance of 177 Fg −1 [43,44]. The comparative performances, including the different concentrations of the electrolytes [45][46][47][48][49], are also summarized in Table 2.  The stability of the electrode is one of the most important issues in energy stora applications. All of the earlier electrochemical results based on CV, GCD and rate cap bility clearly indicate that the CSLDH-2, which has one dimensional nanofibrous m phology, produced the most improved capacitance. The cyclic stability of the optimiz CSLDH-2 electrode was examined by the continuous CD analysis test at 4 Ag −1 curre density over the 2200 cycles. As shown in Figure 13b, the nanofibrous CSLDH-2 electro showed excellent cyclic stability (4 Ag −1 ) up to the 2200 cycles and retained around 89% the specific capacitance as compared to the CSHDS electrode. This better performance the CSLDH-2 demonstrates that it is the presence of the cobalt filler in the CSLDH-2 el trode which helps to stabilize the overall structure of the nanocomposite during t charge-discharge process. The electrochemical performance of the CSLDH-2 electrode comparatively higher than the other two electrodes (CSHDS and CSLDH-1). In additio the retention of the CSLDH-2 electrode highlights its excellent cycling stability and su gests the high reversibility and excellent electrochemical stability of the electrode. Ho ever, the obtained capacitance retention is gradually decreased with the increase in t charge-discharge process, which might be attributed to the electrolyte ions blocking t pores of the electrode materials; in the present case, the electrolyte ions may be trapp in the layers of CSLDH-2 and barred from contributing to further electrochemical red reaction processes in an aqueous electrolyte. Additionally, the Sn/Co might undergo stru tural degradation in the electrolyte during the charge-discharge process. Hence, the s nificant deficiency of capacitance that we noticed might be attributed to the unwant electrochemical redox reaction and structural instability of the electrode in aqueous el trolyte. Efforts are still being made to upgrade the capacitance performance by introdu ing carbonaceous materials, such as graphene and other carbon-based material with d ferent morphology, in work in the near future.

Conclusions
In this study, three different morphologies of Sn/Co nanolayered structures ha been successfully fabricated via host-guest interactions. By intercalation reactions, t guests (cyanate and nitrate anions) were used as pillars for the nanolayers of both cob and tin to build nanolayered structures. By using divalent tin combined with cobalt, t plate morphology of Sn/Co HDS (CSHDS) was formed through nanolayered structur The stability of the electrode is one of the most important issues in energy storage applications. All of the earlier electrochemical results based on CV, GCD and rate capability clearly indicate that the CSLDH-2, which has one dimensional nanofibrous morphology, produced the most improved capacitance. The cyclic stability of the optimized CSLDH-2 electrode was examined by the continuous CD analysis test at 4 Ag −1 current density over the 2200 cycles. As shown in Figure 13b, the nanofibrous CSLDH-2 electrode showed excellent cyclic stability (4 Ag −1 ) up to the 2200 cycles and retained around 89% of the specific capacitance as compared to the CSHDS electrode. This better performance of the CSLDH-2 demonstrates that it is the presence of the cobalt filler in the CSLDH-2 electrode which helps to stabilize the overall structure of the nanocomposite during the charge-discharge process. The electrochemical performance of the CSLDH-2 electrode is comparatively higher than the other two electrodes (CSHDS and CSLDH-1). In addition, the retention of the CSLDH-2 electrode highlights its excellent cycling stability and suggests the high reversibility and excellent electrochemical stability of the electrode. However, the obtained capacitance retention is gradually decreased with the increase in the chargedischarge process, which might be attributed to the electrolyte ions blocking the pores of the electrode materials; in the present case, the electrolyte ions may be trapped in the layers of CSLDH-2 and barred from contributing to further electrochemical redox reaction processes in an aqueous electrolyte. Additionally, the Sn/Co might undergo structural degradation in the electrolyte during the charge-discharge process. Hence, the significant deficiency of capacitance that we noticed might be attributed to the unwanted electrochemical redox reaction and structural instability of the electrode in aqueous electrolyte. Efforts are still being made to upgrade the capacitance performance by introducing carbonaceous materials, such as graphene and other carbon-based material with different morphology, in work in the near future.

Conclusions
In this study, three different morphologies of Sn/Co nanolayered structures have been successfully fabricated via host-guest interactions. By intercalation reactions, the guests (cyanate and nitrate anions) were used as pillars for the nanolayers of both cobalt and tin to build nanolayered structures. By using divalent tin combined with cobalt, the plate morphology of Sn/Co HDS (CSHDS) was formed through nanolayered structures. In the case of using tetravalent tin, the plate structure started its transformation to nanofibers by forming a plate-nanofibrous morphology of Sn/Co LDH (CSLDH-1) through dual intercalation process for both cyanate and nitrate anions. This transformation could be explained by the repulsion forces between the cyanate anions and nitrate anions in the confined space among the cationic nanolayers of Sn/Co. These forces led to the curvature of the nanolayers, forming nanofibers. By changing the percentage of tetravalent tin, the repulsive forces increased to form a nanofibrous morphology for Sn/Co LDH (CSLDH-2). This nanofibrous morphology was favorable for obtaining high specific capacitance and excellent rate stability. In comparison to plate morphology (CSHDS) and plate-fibers (CSLDH-1), the nanofibers (CSLDH-2) electrode showed improved specific capacitance (658 Fg −1 ) and excellent rate stability (89%) which can be attributed to the synergistic effects between the electric double layer capacitive character of the tin and the pseudocapacitance nature of the cobalt, and also indicates that the other morphologies of CSHDS and CSLDH-1 electrodes have poor rate performance due to their slow charge diffusion rates. Secondly, as compared to platelike morphology, nanosize and fibrous morphologies provide larger surface area and better pore size as compared to the CSLDH-1 and CSHDS electrodes and can expose more active sites for the intercalation of the ions during electrochemical analysis.