Development of Ti / Ni Nanolayered Structures to Be a New Candidate for Energy Storage Applications

: Development of electrochemical supercapacitor electrode is the best way to improve the performance and conductivity of the alone materials and support energy storage devices. In this work, cyanate anions have used as building blocks to build series of nanolayered materials based on Ti / Ni layered double hydroxides (LDHs). The structural and morphological characteristics of the prepared Ti / Ni LDHs were examined using di ﬀ erent techniques. The electrochemical supercapacitive behavior of the prepared LDHs was observed in the three-assembly electrochemical cell. These results showed that the optimized ratio of the nickel and titanium plays an important role to enhance the electrochemical performance of the LDHs. The optimized Ti / Ni LDHs, which has the highest content of titanium, showed the highest speciﬁc capacitance (675 F / g) value. In this trend, this LDH also retain a high percentage of the cyclic retention after long cyclic charging-discharging process. The enhanced performance could be due to the double layer structure, enough interplanar distance between the layer, and large number of exposed active site within the double layer structure of the LDHs. Finally, although there are no reports for the electrochemical supercapacitive performance of Ti / Ni LDHs in the literature, it is interesting to produce a new candidate for energy storage applications.


Introduction
Supercapacitor, known as ultra-capacitor or electrochemical capacitor, considers one of the main keys for developing energy storage devices because of its good safety, long cycling life and high-power performance [1][2][3][4][5][6][7][8][9]. According to the mechanisms of charge storage, the materials of electrode have been generally classified into three types, including battery-type electrodes with diffusion-controlled Faradaic processes, pseudo-capacitor electrodes with surface electron-transfer processes, and electrochemical double-layer capacitor (EDLC) electrodes with reversible ion adsorption processes. Because of an increasing the demand of electric vehicles, many authors focused on developing the energy storage devices through constructing hybrid supercapacitors to enhance energy densities without the decline of power densities. It was achieved by combining the EDLC electrodes as negative electrodes with the battery-type electrodes as positive electrodes [10,11]. In this trend, the electrochemical performance of supercapacitors was improved through the battery-type electrodes in the terms of energy density, specific capacitance, and working potential window leading to the balance between chemical (high-power output) and physical (high energy output) characteristics [12][13][14][15][16]. Therefore, various battery-type electrode materials were developed using Fe 3 O 4 , V 2 O 5 , Co 3 O 4 , NiCo 2 S 4 , and NiCo 2 O 4 for supercapacitors [17][18][19]. 2 of 12 Layered double hydroxides (LDHs) belong to a large family of inorganic nanolayered structures consisting of several nanolayers. These nanolayers, which contain di-and tri-valent cations, act as a cationic host because presence of di-with tri-valent metals produces positive charges. By intercalating anions among these nanolayers, nanolayered structures of LDHs are produced through host-guest interaction [20][21][22]. Recently, the applications of LDHs in the field of supercapacitors as battery-type materials have been attracted attention because of their high regulation of dominant compositions without the structure transformation. For instance, Ni-Co-Al-LDHs achieved high specific capacitance by Xiao et al. [23], where 2369 F/g was observed at a current density of 1 A/g. In addition, Jagadale et al. reported that the maximum specific capacitance of Co-Mn LDHs was observed at the current density of 0.7 A/g and was 1063 F/g with 96% cycling stability for 5000 cycles [24]. Moreover, new opportunities for accelerating ion diffusion processes during Faradaic reactions was attractive through the exchangeable characteristic of interlayer anions among the nanolayers of LDHs host to control the inter-planar spacing and interlayer building block [24].
Although, wide variety of materials has tested for supercapacitors [23][24][25][26][27], Ni-Ti LDHs have seldom been investigated in this field. Ni-Ti-cyanate LDHs have not reported, not even by the latest literature available [26,27]. In this trend, the current study focuses on preparation of series of Ni-Ti LDHs. Formation of Ni-Ti LDHs at different reaction times is investigated by different techniques. Furthermore, the effect of the molar ratio of Ni/Ti on formation of LDH structure is examined through intercalation of cyanate anions. The electrochemical behavior of the prepared materials is deeply studied in the field of supercapacitors.

Materials
Nickel (II) chloride hexahydrate, titanium (IV) chloride and urea were acquired from Sigma Aldrich. Nickel (II) chloride hexahydrate powder (SKU 654507) has purity 99.9%. Titanium tetrachloride liquid (SKU 208566) has purity 99.9% with density 1.73 g/mL. Titanium tetrachloride was sensitive for air and strongly dissolved in water with exothermic reaction. Therefore, preparation of the aqueous solution of titanium tetrachloride was carried out in vacuum box. The nickel foam with 1.6 mm thickness, 346 g/m 2 surface density, ≥95 % porosity, and >99.99% purity was purchased from MTI Corporation, USA. Typically, an aqueous solution of titanium tetrachloride (0.024 M) was added to urea solution (1 M) to prepare 750 mL of clear solution. Then, 250 mL of nickel chloride solution (0.095 M) was mixed with the previous solution under vigorous stirring. The temperature of the reaction was adjusted at 80 • C. The molar ratio of Ni:Ti was 4. By filtration and washing, the product was dried at room temperature.
To study the effect of titanium concentration on Ni-Ti LDHs, the previous process was repeated by changing the molar ratio of Ni:Ti to be 3, 4 and 5. The temperature of the process was adjusted to 80 • C for 19 h. The sample was labeled here after as Ni-Ti-Y LDHs, where Y is the Ni/Ti molar ratio.

Three Assembly Electrochemical Cell Setup And Electrode Preparation
The electrochemical performance of the prepared materials was examined in the three-electrode half-cell assembly using Auto lab electrochemical workstation. Platinum sheet assembled in glass rod used as counter electrode (Metrohm), whereas AgCl/Ag electrode was used as reference electrode. The KOH solution was used as electrolytes for the electrochemical measurements. The working Appl. Sci. 2020, 10, 6935 3 of 12 electrode prepared through making the slurry of the 10% carbon black, 10% PVDF, and 80% active material in the NMP solvent. The above slurry was further coated on the washed nickel foam with the effective area of 1 cm 2 and loading of the active material was~2 mg. The coated electrode was further dried in the oven and performance was analyzed using cyclic voltammetry (CV) and Galvanostatic charge discharge methods. Figure 1 showed the X-ray diffraction pattern of Ni-Ti-4 LDHs after reaction time 6 h. It revealed non-crystalline structure. By continuing the reaction time to be 8-14 h, one clear peak started to grow at 0.73 nm. Furthermore, weak peaks were observed at 0.37 nm and 0.27 nm as shown in Figure 1. material in the NMP solvent. The above slurry was further coated on the washed nickel foam with the effective area of 1 cm 2 and loading of the active material was ~2 mg. The coated electrode was further dried in the oven and performance was analyzed using cyclic voltammetry (CV) and Galvanostatic charge discharge methods. Figure 1 showed the X-ray diffraction pattern of Ni-Ti-4 LDHs after reaction time 6 h. It revealed non-crystalline structure. By continuing the reaction time to be 8-14 h, one clear peak started to grow at 0.73 nm. Furthermore, weak peaks were observed at 0.37 nm and 0.27 nm as shown in Figure 1. These peaks are similar to the main peaks of the conventional layered double hydroxides and the natural hydrotalcite. After the reaction time 19-26 h, the X-ray diffraction patterns showed clear peaks at 0.73 nm, 0.37 nm, 0.26 nm and 0.24 nm. These peaks agree with the reflections of 003, 006, 009, and 012 planes of LDH structure. The good agreement between the values corresponding to successive diffractions by basal planes, i.e., d003=2d006=3d009, reveals nanolayered structures with highly packed stacks of brucite-like layers ordered along axis c. Dimension c is calculated as three times the spacing for planes (003), i.e., 2.19 nm. This c dimension is lower than that reported for natural and synthetic hydrotalcite, 2.31 nm [28].

Powder X-ray Diffraction
Comparing with the XRD results of the carbonate-LDHs, the interlayered spacing of the prepared product shifted to lower value from 0.76 nm to 0.73 nm indicting that the interlayered anions are different from carbonate anions. This value is related to the thickness of the brucite-like layers (0.48 nm for hydrotalcite), as well as the size of interlayered anions (and, in some cases, its orientation) and the number of water molecules existing in the interlayer.
To study the effect of water molecules on the interlayered spacing of Ni-Ti-4 LDHs, the samples were dried at room temperature and measured by XRD. Figure 2 showed the X-ray diffraction patterns of the prepared products after different reaction times. They showed that the interlayered These peaks are similar to the main peaks of the conventional layered double hydroxides and the natural hydrotalcite. After the reaction time 19-26 h, the X-ray diffraction patterns showed clear peaks at 0.73 nm, 0.37 nm, 0.26 nm and 0.24 nm. These peaks agree with the reflections of 003, 006, 009, and 012 planes of LDH structure. The good agreement between the values corresponding to successive diffractions by basal planes, i.e., d003=2d006=3d009, reveals nanolayered structures with highly packed stacks of brucite-like layers ordered along axis c. Dimension c is calculated as three times the spacing for planes (003), i.e., 2.19 nm. This c dimension is lower than that reported for natural and synthetic hydrotalcite, 2.31 nm [28].
Comparing with the XRD results of the carbonate-LDHs, the interlayered spacing of the prepared product shifted to lower value from 0.76 nm to 0.73 nm indicting that the interlayered anions are different from carbonate anions. This value is related to the thickness of the brucite-like layers (0.48 nm for hydrotalcite), as well as the size of interlayered anions (and, in some cases, its orientation) and the number of water molecules existing in the interlayer.
To study the effect of water molecules on the interlayered spacing of Ni-Ti-4 LDHs, the samples were dried at room temperature and measured by XRD. Figure 2 showed the X-ray diffraction patterns of the prepared products after different reaction times. They showed that the interlayered spacing shifted from 0.73 nm to 0.75 nm because of presence of more water molecules inside the interlayered spacing. However, the nanolayered structure of the prepared product did not change indicating successive reflections at 0.75 nm, 0.38 nm and 0.26 nm.   The effect of Ni/Ti molar ratio on formation of Ni-Ti LDHs was also investigated as shown in Figure 3. Figure 3 showed that Ni-Ti LDHs are formed with different molar ratios of Ni/Ti; 5, 4 and 3. The XRD patterns revealed the basal reflections of (003), (006), and (009) planes, which are characteristic of LDHs structure. Also, it can be noted that the nanolayered structures are observed for all samples. The effect of Ni/Ti molar ratio on formation of Ni-Ti LDHs was also investigated as shown in Figure 3. Figure 3 showed that Ni-Ti LDHs are formed with different molar ratios of Ni/Ti; 5, 4 and 3. The XRD patterns revealed the basal reflections of (003), (006), and (009) planes, which are characteristic of LDHs structure. Also, it can be noted that the nanolayered structures are observed for all samples.   The effect of Ni/Ti molar ratio on formation of Ni-Ti LDHs was also investigated as shown in Figure 3. Figure 3 showed that Ni-Ti LDHs are formed with different molar ratios of Ni/Ti; 5, 4 and 3. The XRD patterns revealed the basal reflections of (003), (006), and (009) planes, which are characteristic of LDHs structure. Also, it can be noted that the nanolayered structures are observed

Fourier Transform Infrared Spectroscopy
FT-IR technique has used to detect and identify the nature of the functional groups and the interlayered anions of Ni-Ti-4 LDHs as shown in Figure 4. Figure 4 displays the spectra of Ni-Ti LDHs after reaction time 10 h and 19 h.

Fourier Transform Infrared Spectroscopy
FT-IR technique has used to detect and identify the nature of the functional groups and the interlayered anions of Ni-Ti-4 LDHs as shown in Figure 4. Figure 4 displays the spectra of Ni-Ti LDHs after reaction time 10 h and 19 h. The vibration of the hydroxyl groups of LDHs was observed at 3436 cm −1 as a broad absorption band. The broadness of the OH band was due to existence of hydrogen bonds which was confirmed by observing weak bands at 2923 cm −1 and 2852 cm −1 for the OH stretching mode of the hydrogen bonds to the interlayered anions and water molecules [29]. Furthermore, the bending mode band of water molecules was observed at 1635 cm −1 [29]. The insertion of cyanate and isocyanate anions into the Ni-Ti LDHs structure was verified by appearance of two bands. These two bands overlapped and centered at 2217 cm −1 [29][30][31][32]. As can be noted in Figure 4, traces of carbonate anions were also detected by a weak peak at 1459 cm −1 [28]. This weak peak suggests that the IR absorption comes from the carbonates interacting weakly with LDH slabs or just adsorbed on the slab surface. The peak of Ti-OH lattice vibration in the precursor was observed at 669 cm −1 while the Ni-OH lattice vibration was 457 cm −1 [33,34].
The effect of the reaction time on the structure of Ni-Ti LDHs was investigated by the comparison between the spectra of the samples formed after 10 h and 19 h as shown in Figure 4. Figure 4a showed that the sample which was formed after 10 h has the main bands of LDHs structure. By increasing the reaction time, the bands of cyanate and isocyanate anions became sharper and stronger as shown in Figure 4b. It means that 10h is not enough for a complete formation of Ni-Ti LDHs agreeing with XRD results.

Thermal Analyses
The thermal analyses (DTA, TG, and DTG) of Ni-Ti-4 LDHs have used to study the effect of the reaction time on the complete formation of LDHs structure. TG and DTG curves of Ni-Ti LDHs after reaction times 10 h and 19 h are displayed in Figure 5. The total mass losses of both samples were similar. Both samples have lost 25% through four stages. However, the content of both samples was different, where Ni-Ti LDHs after the reaction time 10 h lost 9.7% of its mass during the first two stages indicating removal of the surface and the intercalated water. In case of the sample after the reaction time 19 h, the amount of both surface and intercalated water were only 5%. The decomposition of the interlayered cyanate anions happened through the third stage indicating that the content of cyanate anions increased by increasing the reaction time from 12.3% to 17%. In the final stage, the dehydroxylation process of the nanolayers was gradually achieved up to 600 °C and was 3%. The vibration of the hydroxyl groups of LDHs was observed at 3436 cm −1 as a broad absorption band. The broadness of the OH band was due to existence of hydrogen bonds which was confirmed by observing weak bands at 2923 cm −1 and 2852 cm −1 for the OH stretching mode of the hydrogen bonds to the interlayered anions and water molecules [29]. Furthermore, the bending mode band of water molecules was observed at 1635 cm −1 [29]. The insertion of cyanate and isocyanate anions into the Ni-Ti LDHs structure was verified by appearance of two bands. These two bands overlapped and centered at 2217 cm −1 [29][30][31][32]. As can be noted in Figure 4, traces of carbonate anions were also detected by a weak peak at 1459 cm −1 [28]. This weak peak suggests that the IR absorption comes from the carbonates interacting weakly with LDH slabs or just adsorbed on the slab surface. The peak of Ti-OH lattice vibration in the precursor was observed at 669 cm −1 while the Ni-OH lattice vibration was 457 cm −1 [33,34].
The effect of the reaction time on the structure of Ni-Ti LDHs was investigated by the comparison between the spectra of the samples formed after 10 h and 19 h as shown in Figure 4. Figure 4a showed that the sample which was formed after 10 h has the main bands of LDHs structure. By increasing the reaction time, the bands of cyanate and isocyanate anions became sharper and stronger as shown in Figure 4b. It means that 10h is not enough for a complete formation of Ni-Ti LDHs agreeing with XRD results.

Thermal Analyses
The thermal analyses (DTA, TG, and DTG) of Ni-Ti-4 LDHs have used to study the effect of the reaction time on the complete formation of LDHs structure. TG and DTG curves of Ni-Ti LDHs after reaction times 10 h and 19 h are displayed in Figure 5. The total mass losses of both samples were similar. Both samples have lost 25% through four stages. However, the content of both samples was different, where Ni-Ti LDHs after the reaction time 10 h lost 9.7% of its mass during the first two stages indicating removal of the surface and the intercalated water. In case of the sample after the reaction time 19 h, the amount of both surface and intercalated water were only 5%. The decomposition of the interlayered cyanate anions happened through the third stage indicating that the content of cyanate anions increased by increasing the reaction time from 12.3% to 17%. In the final stage, the dehydroxylation process of the nanolayers was gradually achieved up to 600 • C and was 3%. Appl. Sci. 2018, 8, x FOR PEER REVIEW 6 of 12   Figure 6 showed DTA curves for Ni-Ti LDHs after reaction times 10 h and 19 h. The DTA results confirmed the TG data, where, TG curve of Ni-Ti LDHs after reaction time 10 h showed one endothermic peak at 302 °C agreeing with the endothermic and exothermic effects of the removal of the intercalated water and the oxidation of cyanate anions; respectively. The endothermic peak indicates that the heat released from the oxidation reaction is lower than the heat acquired for water removal. It means that the content of cyanate anions is low inside the sample formed after 10 h. In case of the sample formed after 19 h, two exothermic peaks were observed in the DTA curve at 259 °C and 302 °C indicating oxidation of cyanate and isocyanate anions. The strong exothermic peak indicates the high content of cyanate anions inside Ni-Ti LDHs after reaction time 19 h.

Scanning Electron Microscopy
Scanning electron microscopy of Ni-Ti LDHs with different molar ratios of Ni(II) and Ti(IV) were measured after coating the samples with thin layer of platinum to show clear images. Their images are displayed in Figures 7 and 8.             Figure 7 showed plate-like morphology for Ni-Ti-4 LDHs with medium ratio of Ni/Ti. Furthermore, it indicated that Ni-Ti LDHs contains nanoplatelets having size in the micro scale and thickness in the nano scale. These nanoplatelets built three-dimensional structure of porous system as shown in Figure 7a. By varying the molar ratio of Ni/Ti, the morphology of Ni-Ti LDHs did not change as shown in Figure 8. Figure 8 showed platy morphology with irregular geometry for Ni-Ti-5 LDHs and Ni-Ti-3 LDHs.  Figure 7 showed plate-like morphology for Ni-Ti-4 LDHs with medium ratio of Ni/Ti. Furthermore, it indicated that Ni-Ti LDHs contains nanoplatelets having size in the micro scale and thickness in the nano scale. These nanoplatelets built three-dimensional structure of porous system as shown in Figure 7a. By varying the molar ratio of Ni/Ti, the morphology of Ni-Ti LDHs did not change as shown in Figure 8. Figure 8 showed platy morphology with irregular geometry for Ni-Ti-5 LDHs and Ni-Ti-3 LDHs.
Although many researchers reported that the nanolayered structure of LDHs is limited to the di-and tri-valent metals, this study has succeeded to prepare LDHs based on tetravalent titanium in addition to nickel metal. According to SEM images, Ti/Ni LDHs have plate-like morphology. These plates consist of several layers. The results of X-ray diffraction and FT-IR allowed building a model for Ti/Ni LDHs as shown in Figure 9. The layer thickness is known from literature as 0.48 nm. It means that the interlayered space available for the anions is in the range of 0.25-0.27 according to the main interlayered spacing of the XRD patterns. The interlayered cyanate anions among the nanolayers were confirmed by FTIR results. By comparing with the size of cyanate; 0.34 nm, it can intercalate and attack both sides above and below the nanolayers to neutralize the positive charge (+2). In the same time, it makes angle 52.6 • with the nanolayers. The schematic representation of Ti/Ni LDHs is displayed in Figure 9 agreeing with the experimental results.

Electrochemical Capacitive Performance of Ti/Ni LDHs
The electrochemical performance of the all prepared LDHs based electrode were evaluated by the cyclic voltammetry and galvanostatic charge discharge methods and the results are displayed in the Figures 10 and 11. The initial behavior was examined by the CV and the results showed that all the samples have the pseudocapacitive behavior which was confirmed by the presence of the two visible Appl. Sci. 2020, 10, 6935 8 of 12 peaks in the CV curve. However, the comparative CV curve shows that the optimized LDHs (Ni-Ti-3) exhibited large capacitive area and high capacitance performance as compared to the NiTi-5 LDHs and Ni-Ti-4 LDHs. In addition, it means that the proper ratio of Ti/Ni plays an important role for enhancing the overall performance of the samples as shown in Figure 10a. Increasing or decreasing the ratios are significantly reduced the performance of the electrodes. Figure 10b-d shows the CV profile of the NiTi-5 LDHs, Ni-Ti-4 LDHs, and NiTi-3 LDHs at different scan rate which are further supporting the above comparative results.
location.   Figure 7 showed plate-like morphology for Ni-Ti-4 LDHs with medium ratio of Ni/Ti. Furthermore, it indicated that Ni-Ti LDHs contains nanoplatelets having size in the micro scale and thickness in the nano scale. These nanoplatelets built three-dimensional structure of porous system as shown in Figure 7a. By varying the molar ratio of Ni/Ti, the morphology of Ni-Ti LDHs did not change as shown in Figure 8. Figure 8 showed platy morphology with irregular geometry for Ni-Ti-5 LDHs and Ni-Ti-3 LDHs. Although many researchers reported that the nanolayered structure of LDHs is limited to the di-and tri-valent metals, this study has succeeded to prepare LDHs based on tetravalent titanium in addition to nickel metal. According to SEM images, Ti/Ni LDHs have plate-like morphology. These plates consist of several layers. The results of X-ray diffraction and FT-IR allowed building a model for Ti/Ni LDHs as shown in Figure 9. The layer thickness is known from literature as 0.48 nm. It means that the interlayered space available for the anions is in the range of 0.25-0.27 according to the main interlayered spacing of the XRD patterns. The interlayered cyanate anions among the nanolayers were confirmed by FTIR results. By comparing with the size of cyanate; 0.34 nm, it can intercalate and attack both sides above and below the nanolayers to neutralize the positive charge (+2). In the same time, it makes angle 52.6° with the nanolayers. The schematic representation of Ti/Ni LDHs is displayed in Figure 9 agreeing with the experimental results.

Electrochemical Capacitive Performance of Ti/Ni LDHs
The electrochemical performance of the all prepared LDHs based electrode were evaluated by the cyclic voltammetry and galvanostatic charge discharge methods and the results are displayed in the Figures 10 and 11. The initial behavior was examined by the CV and the results showed that all the samples have the pseudocapacitive behavior which was confirmed by the presence of the two visible peaks in the CV curve. However, the comparative CV curve shows that the optimized LDHs (Ni-Ti-3) exhibited large capacitive area and high capacitance performance as compared to the NiTi-5 LDHs and Ni-Ti-4 LDHs. In addition, it means that the proper ratio of Ti/Ni plays an important role for enhancing the overall performance of the samples as shown in Figure 10a. Increasing or decreasing the ratios are significantly reduced the performance of the electrodes. Figure 10b-d shows the CV profile of the NiTi-5 LDHs, Ni-Ti-4 LDHs, and NiTi-3 LDHs at different scan rate which are further supporting the above comparative results. For the better understanding and for further confirmation of the as prepared LDHs as active material for the electrode applications, the GCD performance was measured and specific capacitance were calculated using the following equations. where C is the calculated specific capacitance in F/g and I represent the applied current. The discharge time represent by the "t" and "m" is the mass of the active materials.  Figure 11 shows the comparative GCD curves of all the electrodes at fixed applied potential. This profile was further used to calculate the specific capacitance in which the Ni-Ti-3 LDHs shows the highest capacitance value compared to the other prepared LDHs (Figure 11a). The Ni-Ti-3 LDHs displayed the 675 F/g specific capacitance whereas the Ni-Ti-4 LDHs and Ni-Ti-5 LDHs exhibited 300 F/g and 352.5 F/g, respectively. This can be also clearly observed by the graph in which the Ni-Ti-5 LDHs and Ni-Ti-4 LDHs exhibited short charging and discharging time whereas the Ni-Ti-3 LDHs shows the very short charging time but exhibited the longer discharge time. The enhanced performance of the optimized electrode is due to the double layer structure, enough interplanar distance between the layer, and large number of exposed active site within the double layer structure of the LDHs. The specific capacitance of all the electrodes at different current densities was also measured in details as shown in Figure 11b For the better understanding and for further confirmation of the as prepared LDHs as active material for the electrode applications, the GCD performance was measured and specific capacitance were calculated using the following equations.
where C is the calculated specific capacitance in F/g and I represent the applied current. The discharge time represent by the "t" and "m" is the mass of the active materials. Figure 11 shows the comparative GCD curves of all the electrodes at fixed applied potential. This profile was further used to calculate the specific capacitance in which the Ni-Ti-3 LDHs shows the highest capacitance value compared to the other prepared LDHs (Figure 11a). The Ni-Ti-3 LDHs displayed the 675 F/g specific capacitance whereas the Ni-Ti-4 LDHs and Ni-Ti-5 LDHs exhibited 300 F/g and 352.5 F/g, respectively. This can be also clearly observed by the graph in which the Ni-Ti-5 LDHs and Ni-Ti-4 LDHs exhibited short charging and discharging time whereas the Ni-Ti-3 LDHs shows the very short charging time but exhibited the longer discharge time. The enhanced performance of the optimized electrode is due to the double layer structure, enough interplanar distance between the layer, and large number of exposed active site within the double layer structure of the LDHs. The specific capacitance of all the electrodes at different current densities was also measured in details as shown in Figure 11b-d. The specific capacitance of Ni-Ti-5 LDHs and Ni-Ti-4 LDHs at current load of 0.6, 1, 2, 3, 5, 7, and 10 A/g were 352.5, 300, 250, 247.5, 200, 175, 105 F/g and 300, 290, 210, 135, 125, 87.5, 70 F/g, respectively. The specific capacitance of Ni-Ti-3 LDHs at current load of 0.6, 1, 2, 3, 5, 7, and 10 A/g were 675, 495, 490, 315, 300, 262.5, and 225 F/g. Again, we can see that the optimized and perfect ration of the Ti/Ni exhibited the highest specific capacitance compared to the other two electrode materials with different ratio. After the electrochemical capacitive performance was studied by CV and GCD, the cyclic stability of the electrode was further evaluated for further confirmation of LDHs as electrode material for energy storage applications. The repeating charge and discharge cyclic stability test were conducted and results are present in Figure 12, which shows that after 1500 continuous cycle of the charge discharge, the Ni-Ti-3 LDHs maintained the stability and shows excellent capacitance retention up to 85%. The comparative stability graph clearly shows that the as prepared Ni-Ti-3 LDHs retained and maintained good stability, which is further confirming the importance of the as prepared active materials. Again, we can see that the optimized and perfect ration of the Ti/Ni exhibited the highest specific capacitance compared to the other two electrode materials with different ratio. After the electrochemical capacitive performance was studied by CV and GCD, the cyclic stability of the electrode was further evaluated for further confirmation of LDHs as electrode material for energy storage applications. The repeating charge and discharge cyclic stability test were conducted and results are present in Figure 12, which shows that after 1500 continuous cycle of the charge discharge, the Ni-Ti-3 LDHs maintained the stability and shows excellent capacitance retention up to 85%. The comparative stability graph clearly shows that the as prepared Ni-Ti-3 LDHs retained and maintained good stability, which is further confirming the importance of the as prepared active materials.

Conclusion
This research achieved a dual aim for optimizing the preparation conditions of Ti/Ni nanolayered structures and producing an active material for the supercapacitor applications. In this trend, series of Ti/Ni based layered double hydroxides (LDHs) with optimized ratio of titanium and nickel have developed through intercalation of cyanate anions using urea hydrolysis. The prepared materials were further characterized by SEM, XRD, TGA, DTA, and FTIR techniques. The performance of LDHs as an active material for the supercapacitor application are also examined in the three electrodes assemble cell and result shows that the Ni-Ti-3 LDHs shows the highest specific capacitance (675 F/g) and excellent cyclic retention, compared to the bare material in fixed experimental conditions. The enhanced performance might be the presence of the large number of exposed active site within the double layer stricture of the LDHs, enhanced conductivity, and enough interplanar distance between the layers. These results showed that the prepared LDHs could be the good option for electrode materials for energy storage applications.

Conclusions
This research achieved a dual aim for optimizing the preparation conditions of Ti/Ni nanolayered structures and producing an active material for the supercapacitor applications. In this trend, series of Ti/Ni based layered double hydroxides (LDHs) with optimized ratio of titanium and nickel have developed through intercalation of cyanate anions using urea hydrolysis. The prepared materials were further characterized by SEM, XRD, TGA, DTA, and FTIR techniques. The performance of LDHs as an active material for the supercapacitor application are also examined in the three electrodes assemble cell and result shows that the Ni-Ti-3 LDHs shows the highest specific capacitance (675 F/g) and excellent cyclic retention, compared to the bare material in fixed experimental conditions. The enhanced performance might be the presence of the large number of exposed active site within the double layer stricture of the LDHs, enhanced conductivity, and enough interplanar distance between the layers. These results showed that the prepared LDHs could be the good option for electrode materials for energy storage applications.