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Carbon materials are generally preferred as anodes in supercapacitors; however, their low capacitance limits the attained energy density of supercapacitor devices with aqueous electrolytes. Here, we report a low-crystalline iron oxide hydroxide nanoparticle anode with comprehensive electrochemical performance at a wide potential window. The iron oxide hydroxide nanoparticles present capacitances of 1,066 and 716Fg−1 at mass loadings of 1.6 and 9.1mgcm−2, respectively, a rate capability with 74.6% of capacitance retention at 30Ag−1, and cycling stability retaining 91% of capacitance after 10,000 cycles. The performance is attributed to a dominant capacitive charge-storage mechanism. An aqueous hybrid supercapacitor based on the iron oxide hydroxide anode shows stability during float voltage test for 450h and an energy density of 104Whkg−1 at a power density of 1.27kWkg−1. A packaged device delivers gravimetric and volumetric energy densities of 33.14Whkg−1 and 17.24Whl−1, respectively.
Due to the fast depletion of fossil fuels and global warming, there is an urgent need for clean energy technologies to supplement and replace the conventional energy sources. At the forefront of clean energy technologies are high-performance energy storage devices, which are needed for the next-generation consumer electronics, biomedical devices and hybrid electric vehicles1,2,3. As a well-known energy storage device, the supercapacitor has attracted tremendous research attention recently due to its high power density (1–10kWkg−1), fast charge and discharge rate (within seconds) and long cycling life (>100,000 cycles)4,5,6,7. Electrical double-layer capacitor (EDLC) materials have been widely used in supercapacitors due to their large specific surface area, high electrical conductivity and low cost8,9,10,11. Although high power density and cycling stability have been realized by these materials, the attained capacitance and energy density are typically low12,13,14. This is because of the charge-storage mechanism for EDLC materials, which is dominated by charge separation at the electrode/electrolyte interface14,15. Pseudocapacitor materials can provide a higher capacitance than EDLC materials due to their surface/near-surface redox reactions1,4,16,17,18.
Currently, the research on supercapacitor is focused on increasing the energy density while retaining comparable high power density19. Asymmetric and hybrid supercapacitors (HSCs) have been extensively studied as a promising strategy to increase the energy density20,21,22,23,24,25,26. A typical HSC consists of both faradaic and capacitive electrodes12,27. This design results in high energy density due to the contributions from the different charge-storage mechanisms and the extended operating potential window in aqueous electroytes (up to 2V)28,29. Faradaic cathode materials have been extensively studied leading to the development of high-performance cathodes for aqueous supercapacitors20,21,30,31,32. For instance, nickel-based oxides have been explored due to their improved electronic conductivity and rich redox reactions, arising from the high electrochemical activity of Ni26,28,33,34. Despite the high performance of these cathode materials, the maximum energy density of their hybrid cells in aqueous electrolytes is largely hindered by the low specific capacitance of commonly used carbon anodes35,36,37. Recently, crystalline iron oxides (Fe2O3, Fe3O4) and iron oxide hydroxide (FeOOH) have been studied as supercapacitor or battery-type anode materials due to their high theoretical capacitance, wide operating potential window, low cost and natural abundance38,39,40,41,42,43,44. Even though significant progress has been achieved for these materials, most of them exhibit short cycle life and poor rate performance. Low-crystalline or amorphous metal oxides are capable of achieving better cycling stability than the high-crystalline counterpart because of their more structural defects and disorder30,45,46,47. As far as we know, it is still a tremendous challenge to obtain anode materials with high capacitance, good rate capability and excellent cycling stability.
In the present work, we report a capacitive dominant FeOOH nanoparticle anode with comprehensive electrochemical performance at a wide potential window. The synthesis of the FeOOH nanoparticle anode involves the hydrothermal growth of iron oxide (α-Fe2O3) nanoparticles on carbon fibre cloth (CFC) and the subsequent electrochemical transformation to low-crystalline FeOOH nanoparticles. The FeOOH anode manifests high specific capacitances at both low and high mass loadings, good rate capability (74.6% capacitance retention at 30Ag−1) and excellent cycling stability (91% capacitance retention after 10,000 cycles). To further evaluate the performance of the FeOOH nanoparticle anode for aqueous HSCs, we also designed the suitable battery-type cathode, nickel molybdate (NiMoO4) using a hydrothermal method. An NiMoO4//FeOOH aqueous hybrid device displays high specific capacitance (273Fg−1), high energy density (104.3Whkg−1) and exceptional stability. Importantly, a packaged device with an active material weight percentage of 35% shows high gravimetric and volumetric energy densities.
We first synthesized Fe2O3 nanoparticles on CFC substrate through a facile hydrothermal method (Supplementary Fig. 1). Fig. 1a shows the X-ray diffraction (XRD) pattern of the Fe2O3. The XRD pattern can be indexed to rhombohedral α-Fe2O3 (JCPDS card no. 00-033-0664) with R-3c space group and lattice parameters of a=b=5.0356Å and c=13.7500Å. The α-Fe2O3 sample was further characterized by Raman spectroscopy (Fig. 1b). A distant band is located at 1,316cm−1 and the narrow bands located at 221 and 492cm−1 can be assigned to the A1g modes, while the bands located at 247, 291, 407 and 607cm−1 are due to the E1g modes of α-Fe2O348,49. The Raman spectrum confirms the existence of α-Fe2O3. The surface area of the α-Fe2O3 was also studied by nitrogen sorption (Supplementary Fig. 2a). The Brunauer–Emmett–Teller (BET) surface area of the α-Fe2O3 is determined to be 41m2g−1.
The morphology of α-Fe2O3 was identified with scanning electron microscopy (SEM) and transmission electron microscopy (TEM). As shown in Fig. 1c, uniformly distributed nanoparticle morphology can be observed. The SEM image at a higher magnification (Fig. 1c, inset) reveals that the nanoparticles are uniform in size and strongly attached to the CFC substrate. From the TEM image (Fig. 1d), the diameter of the nanoparticles is determined to be ~30nm. The high-resolution TEM (HRTEM) image of the α-Fe2O3 nanoparticles is shown in Fig. 1e. Lattice fringes with interplanar spacing of 0.36nm corresponding to the (012) plane of α-Fe2O3 can be clearly discerned. The polycrystalline feature of the α-Fe2O3 nanoparticles is confirmed by the selected area electron diffraction (SAED) pattern (Fig. 1f). It shows a set of concentric rings, which can be indexed to the (104), (113), (116) and (300) diffractions of rhombohedral α-Fe2O3.
The α-Fe2O3 is transformed into low-crystalline FeOOH during electrochemical cycles in the potential range between −1.2 and 0V versus saturated calomel electrode (SCE) (Supplementary Fig. 1). The cyclic voltammetry (CV) curves of the α-Fe2O3 electrode at different cycles in 2M KOH are shown in Fig. 2a. A pair of faradaic peaks positioned at −0.66 and −1.05V versus SCE is observed during the first cycle. The intensity of the peaks gradually reduces during the first ten cycles (defined as activation process) and becomes stable afterwards, which suggests that some changes in crystalline structure have occurred during the first ten cycles. The CV curves after the activation process portray a quasirectangular shape with very broad peaks. To understand the structure changes and charge-storage mechanism of the anode, ex situ XRD, X-ray photoelectron spectroscopy (XPS), SEM and TEM tests were carried out. As shown in Fig. 2b, the α-Fe2O3 is transformed into FeOOH (JCPDS No. 01-077-0247) after ten electrochemical cycles. The α-Fe2O3 phase cannot be recovered in the subsequent discharge process, instead, a mixture of FeOOH and Fe(OH)2 is obtained. SEM images of the transformed FeOOH show that the nanoparticle morphology is well maintained (Supplementary Fig. 3). Also, the TEM and HRTEM images (Fig. 2c,d) further confirm that the α-Fe2O3 is transformed into low-crystalline FeOOH nanoparticles during the activation process. XPS test was carried out to confirm the valence states of the various elements on the surface of α-Fe2O3 after activation. The Fe 2p core-level spectrum (Fig. 2e) shows two characteristic peaks located at 711 and 725eV corresponding to Fe 2p1/2 and Fe 2p3/2 spin orbitals of FeOOH, together with two satellite peaks at 717 and 733eV46,47. The deconvolution of the O 1s core-level spectrum (Fig. 2f) shows three distinct oxygen contributions corresponding to H-O-H (532.7eV), Fe-O-H (531.4eV) and Fe-O-Fe bonds (530.4eV)46,47,50. The H-O-H bond corresponds to water molecule, which suggests that the FeOOH nanoparticles are in hydrated form50. The XPS characterization confirms the electrochemical transformation of α-Fe2O3 nanoparticles to FeOOH nanoparticles, which is highly consistent with the ex situ XRD, SEM and TEM results. According to the above characterizations, the probable transformation reaction and charge-storage mechanism is proposed as follows:
To study the electrochemical performance of the low-crystalline FeOOH nanoparticles, CV and galvanostatic charge/discharge tests were carried out in a three-electrode system with a Pt plate counter-electrode and an SCE reference electrode in 2M KOH electrolyte. Fig. 3a displays the CV curves of the FeOOH nanoparticles tested at different scan rates ranging from 5 to 50mVs−1 in a −1.2 to 0V versus SCE potential window. The quasirectangular shape CV curves of the FeOOH nanoparticle anode denote an electrochemical signature of a typical pseudocapacitive electrode12,27. The symmetric CV curves also indicate that the charge storage process and the redox reactions are reversible. The charge/discharge curves of the FeOOH nanoparticles are shown in Supplementary Fig. 4a. The specific gravimetric and areal capacitances of the FeOOH nanoparticles are calculated from the discharge curves. As displayed in Fig. 3b and Supplementary Fig. 4b, the FeOOH nanoparticles exhibit a capacitance of 1,066Fg−1 (1.71Fcm−2) at 1Ag−1. With the increase of the current density to 30Ag−1, a capacitance of 796Fg−1 (1.27Fcm−2) can be maintained, corresponding to 74.6% of the capacitance at 1Ag−1. Another important performance metric in characterizing supercapacitor electrodes is the mass loading of the active materials51. Considering the mass loading of typical industrial porous carbon electrodes (~10mgcm−2), we tuned the mass loading of the FeOOH anode. The FeOOH anode displays quasirectangular-shaped CV curves and symmetric triangular charge/discharge curves irrespective of the mass loading (Supplementary Fig. 5). With mass loadings of 1.6, 3.0, 5.6 and 9.1mgcm−2, the low-crystalline FeOOH nanoparticle anode displays specific gravimetric capacitances of 1,066, 996, 827 and 716Fg−1 at 1Ag−1, respectively (Fig. 3c). The capacitances of the FeOOH anode decrease with increasing mass loadings; however, they still exhibit good rate capabilities (Supplementary Fig. 6b). The areal and volumetric capacitances of the FeOOH anode (including the volume of the current collector) with a high mass loading of 9.1mgcm−2 can reach as high as 6.5Fcm−2 (Fig. 3c) and 186Fcm−3 (Fig. 3d).
As one of the main parameters for supercapacitors, the long-term cycling stability of the FeOOH anode was studied (Fig. 3e). For the FeOOH anode with a mass loading of 1.6mgcm−2, 91% of the initial capacitance can be retained after 10,000 charge/discharge cycles at 30Ag−1, whereas 86% of the initial capacitance is retained for the anode with a mass loading of 9.1mgcm−2 after 10,000 cycles at 15Ag−1. At 1Ag−1, the FeOOH electrode displays a low voltage drop of 0.0097V, suggesting a low internal resistance (Rs) of the electrode (3.45Ω)52. The Rs and charge transfer resistance (Rct) after the first cycle obtained from the simulation of the Nyquist plot are 3.59 and 0.59Ω, respectively (Fig. 3f). After 10,000 charge/discharge cycles, the Rs increases to 4.10Ω, whereas the Rct reduces to 0.50Ω (Supplementary Table 1). The reduced Rct suggests that the low-crystalline FeOOH facilitates fast diffusion of electrolyte ions, advantageous to the long-term stability of the anode53.
The synthesis of NiMoO4 nanowire cathode was achieved through a hydrothermal method followed by postannealing. The crystallographic phase of NiMoO4 was characterized by XRD analysis. Fig. 4a depicts the Rietveld refined XRD pattern of the NiMoO4. The lattice parameters of NiMoO4 (a=9.5982Å, b=8.7760Å and c=7.6717Å) calculated by Rietveld refinement match well with monoclinic NiMoO4 (JCPDS No. 01-086-0361; a=9.5660Å, b=8.7340Å and c=7.6490Å). The weighted profile Rietveld factor (Rwp) of the NiMoO4 is determined to be 6.853% (Supplementary Table 2). XPS was applied to verify the surface composition of the NiMoO4 nanowires (Supplementary Fig. 7a). The Ni 2p core-level spectrum shows two major peaks with binding energies of 856.19 and 873.92eV, corresponding to Ni 2p1/2 and Ni 2p3/2 of Ni2+, respectively (Supplementary Fig. 7b)54,55. The Mo 3d core-level spectrum presents two characteristic peaks with binding energies of 232.36 and 235.5eV, corresponding to Mo 3d5/2 and Mo 3d3/2 of Mo6+, respectively (Supplementary Fig. 7c)56,57. Last, the deconvolution of O 1s core-level spectrum shows two major oxygen contributions (Supplementary Fig. 7d). The peak located at 530.4eV is associated with the metal-oxygen bond, while the peak at 531.4eV corresponds to the lattice oxygen57.
The morphology of NiMoO4 grown on nickel foam substrate was observed with SEM and TEM. From the low-magnification SEM (Fig. 4b and inset), it can be easily observed that the nanowires are grown on the surface of the nickel foam. A high-magnification SEM (Fig. 4c) shows that the bundled nanowires have needle-like tips. The presence of spaces between adjacent nanowires would enhance the penetration of the electrolyte ions28,58. TEM image of a typical NiMoO4 nanowire is shown in Fig. 4d. The diameter of the NiMoO4 nanowires is determined to be 50–100nm. The HRTEM image of the NiMoO4 nanowire is shown in Fig. 4e, from where the (020) lattice fringes with a lattice spacing of 0.43nm is clearly observed. The polycrystallinity of the NiMoO4 nanowires is confirmed from the SAED pattern (Fig. 4f), as it shows Bragg spots corresponding well with (-205), (204), (-113), (111) and (-313) planes of monoclinic NiMoO4. The NiMoO4 displays a type II isotherm with an H3 hysteresis loop (Supplementary Fig. 2b), and the BET surface area is determined to be 49m2g−1.
Fig. 5a shows the CV curves of NiMoO4 at different scan rates from 1 to 10mVs−1 tested between 0 and 0.5V versus SCE. From the linear sweep voltammetry (LSV) analysis (Supplementary Fig. 8f), it can be observed that oxygen evolution starts at ~0.52V versus SCE in the NiMoO4 electrode. Thus, it is safe for NiMoO4 to be cycled between 0 and 0.5V versus SCE. The charge-storage mechanism in NiMoO4 can be ascribed to faradaic battery-type mechanism from the sharp peaks of the CV curves12,27. The curves show a pair of anodic and cathodic peaks arising from the fast faradaic redox reactions of Ni(II) ← Ni(III) during charge and discharge28,55,56. The NiMoO4 nanowires exhibit very good electrochemical reversibility as evidenced by the near mirror symmetry of both anodic and cathodic peaks55. The specific capacity instead of specific capacitance of the NiMoO4 cathode was calculated from the discharge curves (Supplementary Fig. 9a) to give realistic values of the energy storage and release12,27,36. As shown in Fig. 5b and Supplementary Fig. 9b, the NiMoO4 electrode delivers a specific capacity of 223mAhg−1 (0.33mAhcm−2) at 1Ag−1 and 59% of the capacity can be retained at 30Ag−1 (130mAhg−1, 0.2mAhcm−2). The long-term cycling performance of the NiMoO4 nanowires was also studied. The NiMoO4 nanowires display capacitance retention of 85.1% after 10,000 charge/discharge cycles at 30Ag−1 (Fig. 5c). To provide further insights, EIS was measured to quantify the resistance at the electrode/electrolyte interface (Fig. 5d). The NiMoO4 nanowires display Rs and Rct values of 0.72 and 0.15Ω, respectively.
To further evaluate the practical application of the FeOOH anode, an aqueous HSC was assembled with the NiMoO4 and FeOOH as the cathode and anode, respectively. The NiMoO4 cathode and FeOOH anode are mass balanced at 5.5Ag−1 (Supplementary Fig. 10). As shown in Fig. 6a, series of CV tests are undertaken in different potential windows in 2M KOH to determine the optimal operating potential window of the NiMoO4//FeOOH HSC. Under a potential window of 1.1V, only one anodic peak is visible, implying that there is no contribution from the cathode and the reactions are irreversible (Fig. 6a). Under a wide potential window of 1.9V, the aqueous electrolyte begins to decompose. The optimal potential window of the assembled HSC is determined to be 1.7V. This is in good agreement with the working potential windows of the separate electrodes with respect to the water oxidation and reduction potentials in 2M KOH electrolyte (Supplementary Fig. 8). With the increase of voltage potential from 1.1 to 1.7V at 11.25Ag−1, the capacitance increases from 87.05 to 230.72Fg−1 (Supplementary Fig. 11a), which is mainly due to the increased redox reactions of the electrodes and it can be confirmed from the CV integral area (Fig. 6a). Fig. 6b displays typical CV curves of the HSC at different scan rates in a 1.7V potential window. The CV curves have a non-rectangular shape with a couple of broad reversible redox peaks, which indicate the capacitance mainly comes from the redox reactions. The galvanostatic charge/discharge curves of the NiMoO4//FeOOH HSC at different current densities were tested (Supplementary Fig. 11b). As shown in Fig. 6c, the full HSC delivers a specific capacitance of 273 and 183Fg−1 at a current density of 1.5 and 22.5Ag−1, respectively. The HSC device displays good rate capability with 67% of the capacitance retained in that current density range. Supplementary Fig. 11c shows the long-term cycling stability of the NiMoO4//FeOOH HSC and it retains 80.8% of its initial specific capacitance after 10,000 cycles at a current density of 22.5Ag−1. The float voltage test, a more demanding test than the conventional charge/discharge cycling was also used to study the stability of the NiMoO4//FeOOH HSC in 2M KOH electrolyte59,60. For a test time of 450h, the NiMoO4//FeOOH HSC displays exceptional stability with no loss in capacitance (Fig. 6d).
The energy and power density of the HSC were calculated from the galvanostatic discharge curves and plotted in the Ragone plot (Fig. 6e). The HSC displays a maximum gravimetric energy density of 104.3Whkg−1 at a power density of 1.27kWkg−1 and an energy density of 31Whkg−1 at a maximum power density of 10.94kWkg−1. Volumetric capacitance, volumetric energy and power density are very important parameters for practical applications of supercapacitors51. The NiMoO4//FeOOH packaged device displays high volumetric capacitances; even though the active material mass accounts for just 6.5wt% of the packaged device, the volumetric capacitances still reach 8.24 and 5.53Fcm−3 at 1.5 and 22.5Ag−1, respectively (Fig. 6c). The HSC device also displays a maximum volumetric energy density of 3.15mWhcm−3 at a power density of 38.33mWcm−3 and a maximum volumetric power density of 330.62mwcm−3 at an energy density of 0.68mWhcm−3 (Supplementary Fig. 12). For practical applications, a NiMoO4//FeOOH packaged device with active materials accounting for 35% of the total weight is also assembled. It displays a volumetric capacitance of 42.96Fcm−3, a maximum energy density of 31.44Whkg−1 at a power density of 305Wkg−1 and a maximum power density of 4,976Wkg−1 at an energy density of 12.72Wkg−1 (Supplementary Fig. 13). Last, the packaged device displays maximum volumetric energy and power densities of 17.24 Whl−1 and 2,736.08Wl−1, respectively (Fig. 6f).
Using ex situ XRD, XPS, SEM and TEM tests, it has been unambiguously demonstrated that not only the surface but also the bulk of the α-Fe2O3 nanoparticles can be converted into low-crystalline FeOOH during the electrochemical activation process, which has been rarely reported. The FeOOH anode shows characteristic capacitive CV profiles with broad peaks indicating that the stored charge is mainly pseudocapacitive61. From the CV curves, the capacitive (k1) and diffusion (k2)-controlled contributions to the total capacity at a particular voltage can be separated using the equation shown below61,62,63:
where v is the sweep rate. Fig. 7a–c show a typical separation of capacitive and diffusion currents at scan rates of 1, 2 and 5mVs−1, respectively. As shown in Fig. 7d, the capacitive-controlled process contributes 78.9%, 84.6% and 89.6% of the total charge storage at 1, 2 and 5mVs−1, respectively, suggesting the dominant capacitive charge-storage mechanism in the FeOOH anode. The dominant capacitive storage endows extraordinary high charge storage kinetics and stable cycling performance53,61,62,63. As a result, even at high mass loadings of ~5.6 and 9.1mgcm−2, the FeOOH anode exhibits excellent comprehensive electrochemical performances, which are essential for the practical application of supercapacitors. Compared to carbon materials, the high specific capacitance of the low-crystalline FeOOH nanoparticles validates its selection as the anode for fabricating the full HSC35,36. To the best of our knowledge, the low-crystalline FeOOH nanoparticles display superior electrochemical performances to previously reported iron oxide based nanostructured electrodes (Supplementary Table 3). The FeOOH anode presents the advantages of a wide operating potential window, dominant capacitive charge-storage mechanism and the low-crystalline feature in comparison to several reported iron oxides, which are diffusion-controlled (Supplementary Table 3). A plot of the voltage drops versus current density of both electrodes displays very gentle slopes, which can be ascribed to the low internal resistances and excellent conductivities of the electrodes (Supplementary Fig. 14). The very steep slopes in the Warburg region (Figs 3f and and5d)5d) indicate high ion mobility and diffusion, which is favourable for rate capability and cycling stability.
Compared with recently reported metal oxide//carbon material full supercapacitors, the NiMoO4//FeOOH HSC displays superior specific capacitance20,21,22,23,26,28. Furthermore, the energy density of the assembled HSC exceeds recently reported nickel-based full supercapacitors, such as Ni2Co2S4//G/CS paper (42.3Whkg−1 at 476Wkg−1)20, Ni(OH)2/graphene//porous graphene (77.8Whkg−1 at 174.7Wkg−1)54, FeOOH//Co-Ni-DH (86.4Whkg−1 at 1.83kWkg−1)47, NiMoO4//activated carbon (60.9Whkg−1 at 850Wkg−1)28, Ni-Co-S//graphene film (60Whkg−1 at 1.8kWkg−1)23 and NiMoO4//NiMoO4 (70.7Whkg−1 at 1kWkg−1)33. The excellent electrochemical performance of the NiMoO4//FeOOH HSC may be attributed to the following factors: (1) The dominant capacitive contribution of the low-crystalline FeOOH nanoparticle anode results in high capacitances in a wide potential window, which translates into the high-energy density of the hybrid device. (2) The FeOOH nanoparticles present short ion diffusion paths, which are favourable for fast redox reactions, and the low crystalline structure has the self-adaptive strain-relaxation capability during the charge and discharge processes, leading to high stability. (3) The large surface area of the active materials provides more active sites for charge storage. (4) The direct growth of active materials on conductive substrates eliminates the use of a binder, which often inhibits electrode/electrolyte contact areas and increases the overall resistances of the electrodes. (5) The highly conductive and porous substrates (nickel foam and CFC) provide continuous electronic transport and easy accessibility of the electrolytes to the active materials.
In summary, we have successfully developed low-crystalline FeOOH nanoparticles through a novel strategy involving the hydrothermal growth and the subsequent electrochemical transformation of α-Fe2O3 nanoparticles. The low-crystalline design of the pseudocapacitive anode with high comprehensive performance largely enhances the energy and power densities of the supercapacitor. Therefore, the well-designed low-crystalline FeOOH materials could be a very suitable supercapacitor anode for future practical applications due to its low cost, easy preparation, environmental benignity and high comprehensive electrochemical performance at a wide potential window. An assembled NiMoO4//FeOOH HSC displays a high capacitance of 273Fg−1 at 1.5Ag−1 and a high energy density of 104.3Whkg−1 at a power density of 1.27kWkg−1 in an extended potential window (1.7V), which largely overcomes the present tremendous challenge of the low-energy density of supercapacitors. Our work also provides a promising design direction for optimizing the electrochemical performance of full supercapacitors using various pseudocapacitive materials with suitable reaction potentials.
Fe(NO3)3·9H2O (1.212g) was dissolved in 60ml distilled water and stirred for 2h. Afterwards, the resultant clear solution was transferred into a Teflon-lined stainless-steel autoclave containing precleaned CFC. The hydrothermal process was carried out at 120°C for 24h. After cooling, the substrate was removed and washed with distilled water. The sample was dried at 70°C for 12h to obtain the α-Fe2O3 nanoparticles. The mass of the α-Fe2O3 nanoparticles on the CFCs can be easily tuned by controlling the synthesis conditions. The α-Fe2O3 nanoparticles electrodes were electrochemically cycled in a three-electrode cell system by using the as-synthesized materials on the CFC substrate as the working electrode, Pt plate as counter-electrode and SCE as reference electrode in 2M KOH electrolyte. The α-Fe2O3 nanoparticles electrodes were fully transformed into FeOOH nanoparticles after the tenth cycle in a −1.2 to 0V versus SCE potential window.
The synthesis of NiMoO4 nanowires was achieved by a mild hydrothermal method with postannealing. In a typical synthesis, NiCl2·6H2O (0.725g) was dissolved in 25ml H2O and stirred for 1h, followed by drop-wise addition of 25ml aqueous solution of Na2MoO4·2H2O (0.740g) and stirred for another 2h (all chemicals were used as received without purification). The resultant solution was transferred into a Teflon-lined stainless-steel autoclave containing precleaned nickel foams and kept at 120°C for 12h. The as-synthesized precursor was then ultrasonically cleaned at 50Hz for 5min in distilled water, dried at 70°C overnight and finally annealed in argon at 400°C for 2h at a ramping rate of 5°Cmin−1.
The crystallographic characterization of the as-synthesized samples was performed with a Bruker D8 Advance X-ray diffractometer with a non-monochromatic Cu Ka X-ray source. Field emission SEM images were obtained with a JEOL-7100F microscope. TEM images were collected with a JEM-2100F STEM/EDS microscope. The BET surface area was measured using a Tristar II 3,020 instrument at 77K. Raman spectrum was achieved using a Renishaw RM-1000 laser Raman microscopy system. XPS measurements were performed using a VG Multi Lab 2,000 instrument.
The conductive substrates, nickel foam (2 × 5 × 0.04cm3) and CFCs (2 × 7 × 0.035cm3) were initially weighed before the growth of the active materials. All the samples were washed with distilled water and dried thoroughly at 80°C overnight before being weighed with an analytical balance. The mass of the active materials was determined by the mass difference (before and after drying for the anode; before and after calcination for the cathode) divided by the macroscopic area of the conductive substrates. The mass loading of the NiMoO4 and FeOOH is 1.5 and 1.6mgcm−2, respectively. The thickness of the samples was measured with a vernier caliper.
The electrochemical measurements of the individual electrode samples were carried out in a three-electrode cell system with the as-synthesized materials on the conductive substrates as the working electrode, SCE as reference electrode and Pt plate as counter-electrode in a 2M KOH electrolyte using an electrochemical workstation (CHI 760D).
The specific capacitances of the electrodes and devices were calculated from the galvanostatic discharge curves at different current densities using the formula below.
where Cs (Fg−1) is the specific capacitance, I (A) is the discharge current, Δt (s) is the discharge time, m (g) is the mass of the active material and ΔV is the operating voltage (obtained from the discharge curves excluding the potential drop). The areal capacitance (CA, Fcm−2) of the electrodes was calculated by replacing the mass loading with the surface area of the electrodes (1cm2). The volumetric capacitance (Cv, Fcm−3) of the FeOOH nanoparticle anode was calculated by replacing the mass of the active material with the volume of the electrodes (including the volume of the current collectors).
The specific capacities of the NiMoO4 cathode at different current densities were calculated from the galvanostatic discharge curves according to the equation below
where C (mAhg−1) is the specific capacity, I (mA) is the discharge current and m (g) is the mass of the active material.
Electrochemical impedance spectroscopy was performed under a sinusoidal signal over a frequency range from 0.01 to 105Hz with a magnitude of 10mV. The internal resistance (Rs) was also determined from the galvanostatic discharge curves by dividing the voltage drop at the beginning of the discharge (Vdrop) by the applied constant current, I (A) according to the formula below
A supercapacitor was fabricated with NiMoO4 nanowires as cathode and FeOOH nanoparticles as anode, which were separated with glass fibre filter paper in 2M KOH electrolyte. The overall volume of the NiMoO4//FeOOH HSCs includes the active materials, current collectors and separator.
The mass ratio of the positive to negative electrode is obtained by using the equation below
where m+ and m− are the mass loading of the NiMoO4 and FeOOH electrodes, respectively, C− is the specific capacitance of the FeOOH electrode, C is the specific capacity of the NiMoO4 electrode and ΔV− is the potential window of the FeOOH electrode.
The constant float voltage method was carried out to test the stability of the NiMoO4//FeOOH HSC using a battery test system (LAND CT2001A). In brief, a constant voltage of 1.7V was applied to an assembled supercapacitor device with NiMoO4 and FeOOH electrodes and 2M KOH electrolyte. Three charging/discharging cycles from 0 to 1.7V were performed at a constant current density of 2.5Ag−1 every 10h to quantify the corresponding retaining specific capacitance. The total test time was 450h.
The gravimetric energy density and power density of the as-fabricated HSC were calculated based on the formula shown below
where E (Whkg−1) is the energy density, P (Wkg−1) is the power density, I (A) is the discharge current, V(t) is the discharge voltage excluding the IR drop, m (g) is the total mass of the active material (cathode and anode), dt is the time differential and Δt (s) is the discharge time.
The volumetric capacitance, energy density and power density of the NiMoO4//FeOOH HSC were calculated based on the formulas below
where Cv (Fcm−3) is the volumetric capacitance, I (A) is the discharge current, Δt (s) is the galvanostatic discharge time, ΔV is the voltage range excluding the potential drop, V (cm3) is the total volume of the supercapacitor device (includes cathode, anode and separator), E (mWhcm−3) is the volumetric energy density of the supercapacitor device, V(t) is the discharge voltage excluding the IR drop and P (mWcm−3) is the volumetric power density of the supercapacitor device.
All relevant data supporting the findings of this study are available on request from the corresponding author.
How to cite this article: Owusu, K. A. et al. Low-crystalline iron oxide hydroxide nanoparticle anode for high performance supercapacitors. Nat. Commun. 8, 14264 doi: 10.1038/ncomms14264 (2017).
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Supplementary figures, supplementary tables and supplementary references.
This work was supported by the National Key Research and Development Program of China (2016YFA0202603), the National Basic Research Program of China (2013CB934103), the Programme of Introducing Talents of Discipline to Universities (B17034), the National Natural Science Foundation of China (51521001, 51502226, 21673171), the National Natural Science Fund for Distinguished Young Scholars (51425204), the Fundamental Research Funds for the Central Universities (WUT: 2015-YB-002, 2016III001, 2016III002) and the Students Innovation and Entrepreneurship Training Program (20151049701006). L.B.Q. would like to acknowledge the support from The Monash Centre for Atomically Thin Materials.
The authors declare no competing financial interests.
Author contributions K.A.O. and L.B.Q. contributed equally to this work. L.Q.M., K.A.O. and L.B.Q. conceived and designed the experiments. K.A.O., L.B.Q. and C.Y. carried out most of the experiments and analyzed the data. K.N.Z. carried out the Reitveld XRD characterization. Z.Y.W. and K.A.O. carried out the XPS characterization. K.A.O., L.B.Q., L.Z. and L.Q.M. cowrote and revised the paper. All authors commented on and discussed the results.