Facile synthesis of Mesoporouscobalt Hexacyanoferrate Nanocubes for High-Performance Supercapacitors

Mesoporous cobalt hexacyanoferrate nanocubes (meso–CoHCF) were prepared for the first time through a facile sacrificial template method. The CoHCF mesostructures possess a high specific surface area of 548.5 m2·g−1 and a large amount of mesopores, which enable fast mass transport of electrolyte and abundant energy storage sites. When evaluated as supercapacitor materials, the meso–CoHCF materials exhibit a high specific capacitance of 285 F·g−1, good rate capability and long cycle life with capacitance retention of 92.9% after 3000 cycles in Na2SO4 aqueous electrolyte. The excellent electrochemical properties demonstrate the rational preparation of mesoporous prussian blue and its analogues for energy storage applications.


Introduction
Supercapacitors, also known as electrochemical capacitors, are considered one of the most promising energy storage devices, owing to their desirable properties of high power density, high energy density and excellent cycling stability [1]. Based on the charge-storage mechanism, supercapacitors can be generally classified into two types: electrical double-layer capacitors (EDLCs) and pseudocapacitors. The former stores charges through electrostatic adsorption/desorption at the electrode-electrolyte interface; while the energy of pseudocapacitors comes from rapid Faradaic reactions occurred at the surface of electrode materials [2]. For EDLCs, carbonaceous materials with large surface area are widely used, such as activated carbon [3], carbon nanotubes [4], carbon xerogel [5] and graphene [6]. The most widely investigated electrode materials of pseudocapacitors include conducting polymers and transition-metal oxides or hydroxides [7,8].
As a representative of the metal organic framework materials, prussian blue (PB) can be generally expressed as A x Fe[Fe(CN) 6 ] y ·mH 2 O (A, alkaline metal; 0 < x < 2, y < 1) [9,10]. In the framework of PB, Fe in low-spin and high-spin state bond with six C and six N atoms, respectively, forming face-centered-cube (FCC) crystal structure and resultant open channels [11][12][13]. Prussian blue analogues (PBAs), with similar crystal structures to PB, can be obtained by replacing part or all of the irons by other transition-metal elements (e.g., Co, Ni and Mn) [14,15]. As electrode materials, the open framework of PB or PBAs could provide large interstitial sites for insertion/extraction of alkali metals ions [16]. Besides, the PBAs possess the advantages of relatively higher specific capacitance, environmental friendliness and low cost, which make it promising in the field of energy storage [17]. However, the poor electrical conductivity and serious agglomeration of PBAs' nanoparticles limit the effective utilization of their electrochemical performance [18]. To address this issue, two methods have been developed: (i) combining PBAs with conducting materials [19]; and (ii) increasing the reaction sites of PBAs by reducing the particle size with high specific surface area [20]. There have been a number of studies to synthesize PB/PBA and their composites for supercapacitors [21][22][23][24]. It is worth noting that mesopores are important for mass transport, which determines the accessing capability of electrolyte ions to the intrinsic micro-channels of PB/PBA [25]. However, the synthesis of mesoporous PB/PBAs has scarcely been reported.
In this work, we developed a facile and controllable sacrificial template route to prepare mesoporous cobalt hexacyanoferratenanocubes (meso-CoHCF). The as-prepared meso-CoHCF possesses a high specific surface area of 548.5 m 2 ·g −1 and a large amount of mesopores centered at 4.6 nm. The meso-CoHCF electrodes exhibit a high specific capacitance of 285 F·g −1 at a scan rate of 2 mV·s −1 in neutral Na 2 SO 4 electrolyte, which is much higher than that of the controlled CoHCF nanoparticles (CoHCF, 215 F·g −1 ). nanoparticles limit the effective utilization of their electrochemical performance [18]. To address this issue, two methods have been developed: (i) combining PBAs with conducting materials [19]; and (ii) increasing the reaction sites of PBAs by reducing the particle size with high specific surface area [20]. There have been a number of studies to synthesize PB/PBA and their composites for supercapacitors [21][22][23][24]. It is worth noting that mesopores are important for mass transport, which determines the accessing capability of electrolyte ions to the intrinsic micro-channels of PB/PBA [25]. However, the synthesis of mesoporous PB/PBAs has scarcely been reported.

Characterization of Meso-CoHCF
In this work, we developed a facile and controllable sacrificial template route to prepare mesoporous cobalt hexacyanoferratenanocubes (meso-CoHCF). The as-prepared meso-CoHCF possesses a high specific surface area of 548.5 m 2 ·g −1 and a large amount of mesopores centered at 4.6 nm. The meso-CoHCF electrodes exhibit a high specific capacitance of 285 F·g −1 at a scan rate of 2 mV·s −1 in neutral Na2SO4 electrolyte, which is much higher than that of the controlled CoHCF nanoparticles (CoHCF, 215 F·g −1 ). Figure 1(a-c) exhibits the morphology of the meso-CoHCF sample. From the low magnification field-emission scanning electron microscopy (SEM) image (Figure 1(a)), the meso-CoHCF sample is composed of uniform nanocubes with sizes in the range of 300-500 nm. A closer observation from the high-resolution SEM image (Figure 1(b)) reveals the presence of mesopores on the exterior surface. The porous microstructure is verified by transmission electron microscopy (TEM) imaging, which shows the existence of numerous voids in the interior of the nanocubes. For comparison, CoHCF nanoparticles were synthesized by conventional chemical precipitation method. Figure1 (d-f) show the SEM and TEM images of the CoHCF nanoparticles. It is observed that the irregular CoHCF nanoparticles are of solid morphology. The phase structure of the products is investigated by X-ray diffraction (XRD). As shown in Figure 2(a), the meso-CoHCF and CoHCF samples show identical diffraction pattern, in which the diffraction peaks can be well indexed to the face-centered cubic phase of Co3[Fe(CN)6]2·xH2O [26]. No other diffraction peaks are noted, indicating a high purity of the products. To determine the chemical structure of CoHCF, Fourier-transform infrared (FTIR) spectra were collected. As shown in Figure  2(b), the strong absorption band at 2104 cm −1 is characteristic of PB structure, which can be assigned The phase structure of the products is investigated by X-ray diffraction (XRD). As shown in Figure 2a, the meso-CoHCF and CoHCF samples show identical diffraction pattern, in which the diffraction peaks can be well indexed to the face-centered cubic phase of Co 3 [Fe(CN) 6 ] 2 ·xH 2 O [26]. No other diffraction peaks are noted, indicating a high purity of the products. To determine the Nanomaterials 2017, 7, 228 3 of 9 chemical structure of CoHCF, Fourier-transform infrared (FTIR) spectra were collected. As shown in Figure 2b, the strong absorption band at 2104 cm −1 is characteristic of PB structure, which can be assigned to the stretching vibration of Fe-CN-Co bonds. The absorption peaks at 3407 and 1620 cm −1 can be attributed to the stretching and bending modes of the H−O−H, respectively, indicating the existence of the interstitial water in the crystal lattice of the sample [27].  The elemental components and their chemical states of the meso-CoHCF were examined by Xray photoelectron spectroscopy (XPS) measurements. As shown in Figure 3(a), the full scan spectrum shows the existence of Co, Fe, O, N and C elements in the sample. Two pairs of subpeaks are present in the high-resolution spectra of Fe2p (Figure 3(b)). The binding energies at 723.5 and 710.0 eV can be assigned to the Fe 3+ in [Fe(CN)6] 3+ , while the peaks at 721.1 and 708.2 eV belong to the Fe 2+ in [Fe(CN)6] 4+ [27,28]. The spectrum of N 1s (Figure3(c)) displays a distinct peak located at 397.9 eV, corresponding to the C≡N in [Fe(CN)6] groups [29]. The C 1s spectrum ( Figure.   The porous characteristics of the samples were investigated by N2 adsorption-desorption measurements. Figure 4(a,b) exhibits the resulting isotherms of meso-CoHCF and CoHCF. The meso-CoHCF possesses a large hysteresis loop in the middle P/P0 region, indicating the presence of uniform mesopores. The corresponding Barrett-Joyner-Halenda (BJH) pore-size distribution plots are displayed as inserts in Figure 4. It is noted that the meso-CoHCF sample has uniform mesopore size centered at 4.6 nm. In sharp contrast, the controlled CoHCF sample shows irregular large pores in the range of 10-100 nm, which come from the agglomeration of the nanoparticles. More remarkably, The elemental components and their chemical states of the meso-CoHCF were examined by X-ray photoelectron spectroscopy (XPS) measurements. As shown in Figure 3a, the full scan spectrum shows the existence of Co, Fe, O, N and C elements in the sample. Two pairs of subpeaks are present in the high-resolution spectra of Fe2p ( Figure 3b). The binding energies at 723.5 and 710.0 eV can be assigned to the Fe 3+ in [Fe(CN) 6 ] 3+ , while the peaks at 721.1 and 708.2 eV belong to the Fe 2+ in [Fe(CN) 6 ] 4+ [27,28]. The spectrum of N1 s ( Figure 3c) displays a distinct peak located at 397.9 eV, corresponding to the C≡N in [Fe(CN) 6 ] groups [29]. The C 1s spectrum ( Figure 3d  The elemental components and their chemical states of the meso-CoHCF were examined by Xray photoelectron spectroscopy (XPS) measurements. As shown in Figure 3 [27,28]. The spectrum of N 1s (Figure3(c)) displays a distinct peak located at 397.9 eV, corresponding to the C≡N in [Fe(CN)6] groups [29]. The C 1s spectrum ( Figure.     The porous characteristics of the samples were investigated by N2 adsorption-desorption measurements. Figure 4(a,b) exhibits the resulting isotherms of meso-CoHCF and CoHCF. The meso-CoHCF possesses a large hysteresis loop in the middle P/P0 region, indicating the presence of uniform mesopores. The corresponding Barrett-Joyner-Halenda (BJH) pore-size distribution plots are displayed as inserts in Figure 4. It is noted that the meso-CoHCF sample has uniform mesopore size centered at 4.6 nm. In sharp contrast, the controlled CoHCF sample shows irregular large pores in the range of 10-100 nm, which come from the agglomeration of the nanoparticles. More remarkably, The porous characteristics of the samples were investigated by N 2 adsorption-desorption measurements. Figure 4a,b exhibits the resulting isotherms of meso-CoHCF and CoHCF. The meso-CoHCF possesses a large hysteresis loop in the middle P/P 0 region, indicating the presence Nanomaterials 2017, 7, 228 4 of 9 of uniform mesopores. The corresponding Barrett-Joyner-Halenda (BJH) pore-size distribution plots are displayed as inserts in Figure 4. It is noted that the meso-CoHCF sample has uniform mesopore size centered at 4.6 nm. In sharp contrast, the controlled CoHCF sample shows irregular large pores in the range of 10-100 nm, which come from the agglomeration of the nanoparticles. More remarkably, the Brunauer-Emmett-Teller (BET) specific surface area of the meso-CoHCF is as large as 548.5 m 2 ·g −1 , which is much higher than that of the CoHCF (70.0 m 2 ·g −1 ). The high surface area along with the uniform mesoporous structure of the meso-CoHCF provide more accessible electro-active sites for charge storage and allow for easy transport of electrolyte ions. the Brunauer-Emmett-Teller (BET) specific surface area of the meso-CoHCF is as large as 548.5 m 2 ·g −1 , which is much higher than that of the CoHCF (70.0 m 2 ·g −1 ). The high surface area along with the uniform mesoporous structure of the meso-CoHCF provide more accessible electro-active sites for charge storage and allow for easy transport of electrolyte ions.

Electrochemical Performance
The electrochemical properties of the meso-CoHCF electrode were evaluated by cyclic voltammetry (CV) and galvanostatic charge/discharge techniques in 0.5 M Na2SO4 aqueous electrolyte. Figure 5 shows the CV curves of the meso-CoHCF and CoHCF electrodes at various scan rates. Both electrodes exhibit typical pseudocapacitive behavior, which features a pair of redox peaks associated with transition between Fe 2+ and Fe 3+ in CoHCF [30]. The symmetric peak shape indicates good reaction reversibility. Compared to the CoHCF electrode ( Figure 5(b)), the CV shape of the meso-CoHCF electrode is well maintained as the scan rate increases to 30 mV·s −1 , indicating better rate capability of the meso-CoHCF electrode with small polarization. The larger current density of the meso−CoHCF electrode at each scan rate manifests a higher specific capacitance. In addition, it is interesting to note that the high-specific-surface-area meso-CoHCF electrode exhibits an approximately rectangular CV shape in the high potential region of 0.8-1.0 V, as shown in Figure 5(c), which is totally different from the CoHCF electrode, demonstrating that there are some electrochemical double layer (EDL) capacitance contributing to the overall capacitance. More importantly, the specific capacitance of the meso-CoHCF electrode is as high as 285 F·g −1 at 2 mV·s −1 , which is much higher than that of the controlled electrode (215 F·g −1 ). Moreover, the meso-CoHCF electrode exhibit better capacitance performance (e.g., 272 F·g −1 at 5 mV·s −1 ) than the reported manganese hexacyanoferrat/manganese dioxide (MnHCF/MnO2) composites electrode (225.6 F g −1 at 5 mV·s −1 ) [21], CoHCF nanoparticles electrode (250 F·g −1 at 5 mV·s −1 ) [24], meso-NiHCF (184 F·g −1 at 5 mV·s −1 ) and meso-CuHCF (243 F·g −1 at 5 mV·s −1 ) [23].

Electrochemical Performance
The electrochemical properties of the meso-CoHCF electrode were evaluated by cyclic voltammetry (CV) and galvanostatic charge/discharge techniques in 0.5 M Na 2 SO 4 aqueous electrolyte. Figure 5 shows the CV curves of the meso-CoHCF and CoHCF electrodes at various scan rates. Both electrodes exhibit typical pseudocapacitive behavior, which features a pair of redox peaks associated with transition between Fe 2+ and Fe 3+ in CoHCF [30]. The symmetric peak shape indicates good reaction reversibility. Compared to the CoHCF electrode (Figure 5b), the CV shape of the meso-CoHCF electrode is well maintained as the scan rate increases to 30 mV·s −1 , indicating better rate capability of the meso-CoHCF electrode with small polarization. The larger current density of the meso−CoHCF electrode at each scan rate manifests a higher specific capacitance. In addition, it is interesting to note that the high-specific-surface-area meso-CoHCF electrode exhibits an approximately rectangular CV shape in the high potential region of 0.8-1.0 V, as shown in Figure 5c, which is totally different from the CoHCF electrode, demonstrating that there are some electrochemical double layer (EDL) capacitance contributing to the overall capacitance. More importantly, the specific capacitance of the meso-CoHCF electrode is as high as 285 F·g −1 at 2 mV·s −1 , which is much higher than that of the controlled electrode (215 F·g −1 ). Moreover, the meso-CoHCF electrode exhibit better capacitance performance (e.g., 272 F·g −1 at 5 mV·s −1 ) than the reported manganese hexacyanoferrat/manganese dioxide (MnHCF/MnO 2 ) composites electrode (225.6 F·g −1 at 5 mV·s −1 ) [21], CoHCF nanoparticles electrode (250 F·g −1 at 5 mV·s −1 ) [24], meso-NiHCF (184 F·g −1 at 5 mV·s −1 ) and meso-CuHCF (243 F·g −1 at 5 mV·s −1 ) [23]. Figure 6a,b shows the galvanostatic charge/discharge curves of the meso-CoHCF and CoHCF electrodes at different current densities from 0.5 to 10 A·g −1 . Both curves exhibit a long charge/discharge voltage plateau at 0.3-0.6 V, which is consistent with the redox peaks in CV curves. The symmetric charge/discharge profiles indicate a high Coulombic efficiency. Figure 6c plots the specific capacitance of the meso-CoHCF and CoHCF electrodes at various current densities. The specific capacitance of both electrodes decreases with the increase of the current density due to the reduced diffusion time at a high current rate [31,32]. It is noted that the meso-CoHCF electrode can deliver a highspecific capacitance of 273 F·g −1 at 0.5 A·g −1 , and sustains an excellent capacitance retention of 73.6% even at 10 A·g −1 . However, the controlled CoHCF electrode can only deliver specific capacitance of 212 and 119 F·g −1 at 0.5 and 10 A·g −1 , respectively. The higher specific capacitance along with the better rate capability of the meso-CoHCF electrode can be attributed to the unique porous structure: (i) the higher BET specific surface area provides more accessible electro-active sites for charge storage; and (ii) the uniform mesopores facilitate fast mass transport of electrolyte ions throughout the electrode for better reaction kinetics. good reaction reversibility. Compared to the CoHCF electrode ( Figure 5(b)), the CV shape of the meso-CoHCF electrode is well maintained as the scan rate increases to 30 mV·s −1 , indicating better rate capability of the meso-CoHCF electrode with small polarization. The larger current density of the meso−CoHCF electrode at each scan rate manifests a higher specific capacitance. In addition, it is interesting to note that the high-specific-surface-area meso-CoHCF electrode exhibits an approximately rectangular CV shape in the high potential region of 0.8-1.0 V, as shown in Figure 5(c), which is totally different from the CoHCF electrode, demonstrating that there are some electrochemical double layer (EDL) capacitance contributing to the overall capacitance. More importantly, the specific capacitance of the meso-CoHCF electrode is as high as 285 F·g −1 at 2 mV·s −1 , which is much higher than that of the controlled electrode (215 F·g −1 ). Moreover, the meso-CoHCF electrode exhibit better capacitance performance (e.g., 272 F·g −1 at 5 mV·s −1 ) than the reported manganese hexacyanoferrat/manganese dioxide (MnHCF/MnO2) composites electrode (225.6 F g −1 at 5 mV·s −1 ) [21], CoHCF nanoparticles electrode (250 F·g −1 at 5 mV·s −1 ) [24], meso-NiHCF (184 F·g −1 at 5 mV·s −1 ) and meso-CuHCF (243 F·g −1 at 5 mV·s −1 ) [23].  charge/discharge voltage plateau at 0.3-0.6 V, which is consistent with the redox peaks in CV curves. The symmetric charge/discharge profiles indicate a high Coulombic efficiency. Figure 6(c) plots the specific capacitance of the meso-CoHCF and CoHCF electrodes at various current densities. The specific capacitance of both electrodes decreases with the increase of the current density due to the reduced diffusion time at a high current rate [31,32]. It is noted that the meso-CoHCF electrode can deliver a highspecific capacitance of 273 F·g −1 at 0.5 A·g −1 , and sustains an excellent capacitance retention of 73.6% even at 10 A·g −1 . However, the controlled CoHCF electrode can only deliver specific capacitance of 212 and 119 F·g −1 at 0.5 and 10 A·g −1 , respectively. The higher specific capacitance along with the better rate capability of the meso-CoHCF electrode can be attributed to the unique porous structure: (i) the higher BET specific surface area provides more accessible electroactive sites for charge storage; and (ii) the uniform mesopores facilitate fast mass transport of electrolyte ions throughout the electrode for better reaction kinetics.
To further understand the electrochemical behavior of the electrodes, electrochemical impedance spectrum (EIS) measurements were performed and the resulting Nyquist plots are shown in Figure 6(d). The EIS data can be fitted using an equivalent circuit model (insert). It can be observed that the EIS curves are composed of a semicircle in the high frequency region and a sloped line in the low frequency region. The first x-intercept on the real axis (Z') represents the bulk resistance of the electrode (Rs), and the diameter of the semicircle corresponds to the charge-transfer resistance (Rct) [33]. Notably, both Rs (4.9 Ω) and Rct (3.2 Ω) of the meso-CoHCF electrode are much smaller than that of the CoHCF electrode (i.e., 6.1 and 4.3 Ω). The porous structure of the meso-CoHCF electrode provides more accessible sites for the charges accumulated at the surface, thereby resulting in a higher double layer capacitance (Cdl) of around 85 μF than that of the CoHCF electrode (16 μF) [4]. In addition, the sloped line is associated with the electrolyte diffusion/transport into the porous electrode [32,33]. Clearly, the meso-CoHCF electrode possesses much more vertical shape, indicating lower diffusion resistance. It is anticipated that the lower internal and diffusion resistance of the meso-CoHCF electrode renders fast reaction kinetics for better power delivery.  To further understand the electrochemical behavior of the electrodes, electrochemical impedance spectrum (EIS) measurements were performed and the resulting Nyquist plots are shown in Figure 6d. The EIS data can be fitted using an equivalent circuit model (insert). It can be observed that the EIS curves are composed of a semicircle in the high frequency region and a sloped line in the low frequency region. The first x-intercept on the real axis (Z') represents the bulk resistance of the electrode (R s ), and the diameter of the semicircle corresponds to the charge-transfer resistance (R ct ) [33]. Notably, both R s (4.9 Ω) and R ct (3.2 Ω) of the meso-CoHCF electrode are much smaller than that of the CoHCF electrode (i.e., 6.1 and 4.3 Ω). The porous structure of the meso-CoHCF electrode provides more accessible sites for the charges accumulated at the surface, thereby resulting in a higher double layer capacitance (C dl ) of around 85 µF than that of the CoHCF electrode (16 µF) [4]. In addition, the sloped line is associated with the electrolyte diffusion/transport into the porous electrode [32,33]. Clearly, the meso-CoHCF electrode possesses much more vertical shape, indicating lower diffusion resistance. It is anticipated that the lower internal and diffusion resistance of the meso-CoHCF electrode renders fast reaction kinetics for better power delivery.
Good cycling stability is an important criterion for supercapacitors in practical applications. Figure 7 shows the cycling performance of the meso-CoHCF and CoHCF electrodes at a large current density of 10 A·g −1 . The meso-CoHCF electrode retains 92.9% of the initial capacitance after 3000 cycles, revealing long-term cycling stability. By contrast, the CoHCF electrode shows a serious capacitance degradation of 26.9% over the 3000-cycle test. The better cycling stability of the meso-CoHCF electrode may benefit from the voidspace in the interior of the nanocubes, which can accommodate the possible volume expansion and contraction during the long-term operation. To confirm it, the morphology of the meso-CoHCF electrode after cycling test is characterized. As shown in the inset of Figure 7, the nanocubes are well maintained after cycling, indicating the robust structure of the meso-CoHCF. Good cycling stability is an important criterion for supercapacitors in practical applications. Figure 7 shows the cycling performance of the meso-CoHCF and CoHCF electrodes at a large current density of 10 A·g −1 . The meso-CoHCF electrode retains 92.9% of the initial capacitance after 3000 cycles, revealing long-term cycling stability. By contrast, the CoHCF electrode shows a serious capacitance degradation of 26.9% over the 3000-cycle test. The better cycling stability of the meso-CoHCF electrode may benefit from the voidspace in the interior of the nanocubes, which can accommodate the possible volume expansion and contraction during the long-term operation. To confirm it, the morphology of the meso-CoHCF electrode after cycling test is characterized. As shown in the inset of Figure 7, the nanocubes are well maintained after cycling, indicating the robust structure of the meso-CoHCF.

Materials and Methods
Materials Synthesis: All chemical reagents were analytical grade and purchased from Sinopharm Chemical Reagent Co., Ltd. (Shanghai, China). In a typical synthesis procedure of the meso-CoHCF, 0.4 g of polyvinylpyrrolidone (PVP) and 100 mg of MnSO4H2O were dissolved in 10 mL ethanol and 10 mL H2O, respectively, under stirring for 30 min to form a homogeneous solution. Next, 10 mL of 0.03 M potassium ferricyanide (K3Fe(CN)6) was added in 3 min and kept under stirring overnight to form MnHCF template. Then, 10 mL of 0.045 M Co(NO3)26H2O was mixed with the above suspension and let stand for 5 h at 50 °C. Finally, the meso-CoHCF products were obtained after filtration (the pore diameter of filter paper was ~0.45 μm) and washing with deionized water and finally drying at 80 °C for 12 h. For comparison, CoHCF nanoparticles were prepared by directly mixing 20 mL of 15 mM Co(NO3)2 with 20 mL 10 mM K3Fe(CN)6 under stirring for 3 h. The precipitates were filtered, rinsed and dried using a similar process. Materials Characterization: The crystalline structures of the as-prepared products were characterized by X-ray powder diffraction (XRD, X'Pert Pro MPD, Philips, Almelo, The Netherlands). The Fouriertransform infrared (FT-IR, Nicolet iS50, Thermo Fisher Scientific, Waltham, MA, USA) spectra were collected in the region from 800 to 4000 cm −1 to detect the chemical components of the samples. X-ray photoelectron spectroscopy (XPS, ESCALAB 250Xi, Thermo Scientific, Waltham, MA, USA) measurements were applied to investigate the elemental composition and surface chemistry. The morphology of the samples was observed with field emission scanning electron microscopy (FE-SEM, FEI NanoSEM 450, FEI, Portland, OR, USA) and transmission electron microscopy (TEM, FEI Tecnai F30G2, FEI, Portland, OR, USA). The porous characteristics of the products was measured by N2adsorption-desorption isotherms (ASAP 2020, Mike, Norcross, GA, USA). The specific surface area was calculated using the BET method while the pore size distribution was determined by BJH model.

Materials and Methods
Materials Synthesis: All chemical reagents were analytical grade and purchased from Sinopharm Chemical Reagent Co., Ltd. (Shanghai, China). In a typical synthesis procedure of the meso-CoHCF, 0.4 g of polyvinylpyrrolidone (PVP) and 100 mg of MnSO 4 H 2 O were dissolved in 10 mL ethanol and 10 mL H 2 O, respectively, under stirring for 30 min to form a homogeneous solution. Next, 10 mL of 0.03 M potassium ferricyanide (K 3 Fe(CN) 6 ) was added in 3 min and kept under stirring overnight to form MnHCF template. Then, 10 mL of 0.045 M Co(NO 3 ) 2 6H 2 O was mixed with the above suspension and let stand for 5 h at 50 • C. Finally, the meso-CoHCF products were obtained after filtration (the pore diameter of filter paper was~0.45 µm) and washing with deionized water and finally drying at 80 • C for 12 h. For comparison, CoHCF nanoparticles were prepared by directly mixing 20 mL of 15 mM Co(NO 3 ) 2 with 20 mL 10 mM K 3 Fe(CN) 6 under stirring for 3 h. The precipitates were filtered, rinsed and dried using a similar process.
Materials Characterization: The crystalline structures of the as-prepared products were characterized by X-ray powder diffraction (XRD, X'Pert Pro MPD, Philips, Almelo, The Netherlands). The Fourier-transform infrared (FT-IR, Nicolet iS50, Thermo Fisher Scientific, Waltham, MA, USA) spectra were collected in the region from 800 to 4000 cm −1 to detect the chemical components of the samples. X-ray photoelectron spectroscopy (XPS, ESCALAB 250Xi, Thermo Scientific, Waltham, MA, USA) measurements were applied to investigate the elemental composition and surface chemistry. The morphology of the samples was observed with field emission scanning electron microscopy (FE-SEM, FEI NanoSEM 450, FEI, Portland, OR, USA) and transmission electron microscopy (TEM, FEI Tecnai F30G2, FEI, Portland, OR, USA). The porous characteristics of the products was measured by N 2 adsorption-desorption isotherms (ASAP 2020, Mike, Norcross, GA, USA). The specific surface area was calculated using the BET method while the pore size distribution was determined by BJH model.
Electrochemical Measurements:The electrochemical tests of meso-CoHCF electrodes were performed on an electrochemical workstation (Solartron 1260 + 1287, Bognor Regis, West Sussex, UK) with a three-electrode configuration system. For the preparation of the working electrode, the active materials, carbon black and polytetrafluoroethylene (PTFE) were mixed with a mass ratio of 7:2:1 and stirred for 2 h. The working electrode was yielded after uniformly painting the above slurry on the nickel foam (1 × 2 cm) and drying at 90 • C for 12 h in an oven. Platinum foil and saturated calomel electrode (SCE) served as counter electrode and reference electrode, respectively, and a 0.5 M Na 2 SO 4 aqueous solution was employed as electrolyte. The mass loading of active materials on the working electrode was around 2.0 mg·cm −2 . The cyclic voltammetry (CV) and galvanostatic charge-discharge techniques were employed within a potential window ranging from 0.0 to 1.0 V. to evaluate the electrochemical performance of the working electrodes [34]. The electrochemical impedance spectroscopy (EIS) measurements were conducted in the frequency range of 10 kHz to 0.01 Hz.

Conclusions
A facile chemical-processing method has been developed in our work to prepare the mesoporous CoHCF nanocubes for supercapcitors. The meso-CoHCF with size between 300 and 500 nm show a high specific surface area of 548.5 m 2 ·g −1 and sufficient meso-channels, which not only offers abundant electro-active sites but also facilitates the mass transport of electrolyte. The meso-CoHCF electrodes exhibit a high specific capacitance of 285 F·g −1 at a scan rate of 2 mV·s −1 and excellent rate capability in Na 2 SO 4 aqueous electrolyte. In addition, the capacitance retention is as high as 92.9% after 3000 cycles at a large current density of 10 A·g −1 . The high specific capacitance, good rate capability and long cycle life makethe meso-CoHCFpromising as supercapacitor electrode materials for practical applications.