High-Performance Asymmetric Supercapacitor Designed with a Novel

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High-performance asymmetric supercapacitor designed with a novel NiSe@MoSe nanosheet arrays and nitrogen-doped carbon nanosheet 2

Hui Peng, Jiezi Zhou, Kanjun Sun, Guofu Ma, Zhiguo Zhang, Enke Feng, and Ziqiang Lei ACS Sustainable Chem. Eng., Just Accepted Manuscript • Publication Date (Web): 02 Jun 2017 Downloaded from http://pubs.acs.org on June 3, 2017

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ACS Sustainable Chemistry & Engineering

High-performance asymmetric supercapacitor designed with a novel NiSe@MoSe2 nanosheet arrays and nitrogen-doped carbon nanosheet Hui Peng,a Jiezi Zhou,a Kanjun Sun,b Guofu Ma*a, Zhiguo Zhang,a Enke Fenga and Ziqiang Lei*a

a

Key Laboratory of Eco-Environment-Related Polymer Materials of Ministry of Education, Key

Laboratory of Polymer Materials of Gansu Province, College of Chemistry and Chemical Engineering, Northwest Normal University, 967 Anning East Road, Lanzhou 730070, China. b

College of Chemistry and Environmental Science, Lanzhou City University, 11 Jiefang Road,

Lanzhou, 730070, China.

*Corresponding author: [email protected] (G. Ma); [email protected] (Z. Lei)

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ABSTRACT Herein, a novel asymmetric supercapacitor (ASC) with high energy density is fabricated based on the NiSe@MoSe2 nanosheet arrays and the nitrogen-doped pomelo mesocarps-based carbon nanosheet (N-PMCN) as positive electrode and negative electrode, respectively. The novel NiSe@MoSe2 nanosheet arrays are designed and prepared by a facile one-step hydrothermal growth method from nickel foam as nickel precursor and nucleation framework. The N-PMCN is prepared by simultaneous CaCl2 activation and urea nitrogen-doped processes from thepomelo mesocarps as biomass-based carbon precursor. Because of the unique nanosheet arrays architecture of NiSe@MoSe2 and interconnected sheet-like porous morphology with high nitrogen contents (~9 wt%) of N-PMCN, they exhibit maximum specific capacity of 128.2 mAh g-1 and high specific capacitance of 223 F g-1 at a current density of 1 A g-1, respectively. Moreover, the assembled novel NiSe@MoSe2//N-PMCN ASC device with a maximum operating voltage of 1.65 V has demonstrated a high energy density of 32.6 Wh kg-1 at a power density of 415 W kg-1, and outstanding cycling stability with 91.4% capacitance retention after 5000 cycles in aqueous electrolyte.

KEYWORDS: Asymmetric supercapacitors, Molybdenum selenide, Nickel selenide, Carbon nanosheet

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INTRODUCTION Supercapacitors have attracted great interest as one of the most promising energy storage devices to alleviate the environmental and energy challenges due to their unique properties including high power density, long cycling lifetime and high safety performance.1-3 Unfortunately, they suffer from a lower specific energy than that of lithium-ion batteries and fuel cells, which has greatly restricted their industrial applications.4-5 The energy density (E) is usually rely on device capacitance (C) and operating voltage (V) according to the general formula E = 1/2CV2. Therefore, to enhance the E of supercapacitors while retaining their intrinsic high power density, both C and V should be crucial to improve.6 As we all known, the C is mainly rely on the inherent properties of electrode materials, including superior electrical conductivity, high chemical stability, unique nanostructure architecture, large specific surface area and possess multiple oxidation states (for transition metal compounds).5,7-9 In general, a large operating voltage can be achieved by selecting organic electrolytes since their stability window up to 2.5~3.0 V.10 Moreover, to develop aqueous asymmetric supercapacitors (ASCs) is an effective alternative approach to boost the operating voltage of supercapacitors, because the organic electrolytes are usually lower conductivity, more expensive and flammable than aqueous electrolytes.5,11 ASCs are usually combined with pseudocapacitive (faradaic battery-type) positive materials and porous carbon (capacitive-type) negative materials, which could utilize their different potential windows of positive and negative electrodes in same aqueous electrolytes.12-14 As a consequence, ASCs not only have a wide operating voltage, but also possess the advantages of both advanced batteries (high energy density) and supercapacitors (high power density and long cycling lifetime). In order to improve the electrochemical performance of ASCs, considerable efforts are devoted to design of novel positive and negative electrode materials with considerable electrochemical performances.5 Recently, two-dimensional (2D) transition metal chalcogenides have emerged as a new promising class of faradaic battery-type electrode materials due to their earth-abundant nature

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and unique physicochemical properties, including metallic-like conductivity, multiply available oxidation states and special sheet-like architectures.16-18 Some metal chalcogenides, including MoS2, NiS, GeSe2 and Co0.85Se with unique 2D hierarchical nanostructures, have been investigated as novel positive electrode materials for supercapacitors.16,19-21 Similarly, MoSe2 is a typical transition metal selenides and the properties are also similar to the MoS2, which both possess graphene-like nanosheets structures and the Mo ions deliver the alteration of oxidation states from +2 to +6, rendering additional pseudocapacitance ability.18 However, isolated MoSe2 are rarely studied to be applied as active materials individually for supercapacitors since they are easily agglomerated because of van der Waals forces.22 Theoretically, fabrication of a new hybrid system via vertical growth of MoSe2 nanosheets onto the conductive matrix to form composite materials with unique heterointerfaces is a feasible way to prevent the aggregation of nanosheets and facilitate a fast and efficient interfacial charge transfer, which is critical to improve the supercapacitive performance.23 Another typical transition metal selenide, nickel selenide, is also an especially promising pseudocapacitor electrode material candidate, owing to the good electrical conductivity, variety of oxidation states and high theory specific capacitance.24-25 In fact, the crystallographic structure of hexagonal nickel selenide matches well with that of the hexagonal MoSe2 because these two transition metal selenides have the same space group (P63/mmc), thus they can provide superior candidates for the construction of a new hybrid system.23 Therefore, constructing the nickel selenide/MoSe2 nanosheets-based hybrid material is promising for the creation of high-performance positive electrode material for supercapacitors. Correspondingly, carbonaceous materials with special architecture (e.g., 2D nanosheets and 3D nanoporous network) are investigated extensively as desirable negative electrode materials due to their high electrical conductivity, large specific surface area and superior electrochemical stability.26-27 Recently, 2D carbon-based nanomaterials, especially nitrogen-doped biomass-based porous carbon nanosheets, have attracted attentions as active materials for high-performance supercapacitors, because it not only provides most features of

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conventional carbon nanomaterials, but also possesses unique 2D interconnection sheet-like porous morphology and high nitrogen contents to increase the surface wettability and electrical conductivity of carbon electrode materials.27-29 In this work, we aim at designing advanced electrode materials with high energy storage properties to develop novel aqueous asymmetric supercapacitors (ASCs) with large output voltage and deliver high energy density. A novel ASC device is designed and fabricated by using a NiSe@MoSe2 nanosheet arrays as a positive electrode and a nitrogen-doped pomelo mesocarpsbased carbon nanosheet (N-PMCN) as a negative electrode in safe KOH aqueous electrolyte. For the positive electrode, the NiSe@MoSe2 with unique hierarchical nanosheet arrays structures can provide large number of exposed reaction active sites and utilize continuous transport pathways in uniform vertical direction to facilitate electrolyte ions diffusion, thus to obtain a large capacitance and high rate capability. For the negative electrode, the N-PMCN with interconnected 2D nanosheet architectures and large specific surface area as well as high nitrogen doping level would facilitate a fast charge transport and lead to remarkable electrochemical energy storage characteristics. Based on the complementary operating potential window between NiSe@MoSe2 and N-PMCN, the asfabricated ASC device (NiSe@MoSe2//N-PMCN) can operate stably of 1.65 V with a high energy density of 32.6 Wh kg-1 at a power density of 415 W kg-1. Moreover, the NiSe@MoSe2//N-PMCN ASC device also possesses outstanding cycling stability of 91.4% capacity retention after 5000 cycles. EXPERIMENTAL Materials Sodium molybdate (Na2MoO4·2H2O) was purchased from Tianjing Chemical Co., Ltd, China. Selenium powder (Se, 99.9%), hydrazine hydrate (N2H4·H2O, 85%), and potassium hydroxide (KOH) were purchased from Sinopharm Chemical Reagent Co., Ltd, China. Calcium chloride (CaCl2) and urea ((NH2)2CO) were purchased from Aladdin Ltd, Shanghai, China. Pomelo mesocarps (the

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pomelo was grown in the Guangdong province, south China region) was treated with dilute HCl (0.2 M) solution and washed with deionized water subsequently, and then dried and smashed before the experiment. Nickel foam was purchased from MTI Corporation and further purification treated with a 5% HCl solution and ethanol sequentially to remove the oxide layer on the surface before used. Synthesis of NiSe@MoSe2 nanosheet arrays The NiSe@MoSe2 nanosheet arrays were prepared using a facile hydrothermal method without any surfactants. In a typical synthesis, 0.4 g of Se powder was dissolved in 2 ml of N2H4·H2O under violent stirring. In a separate flask, 0.06 g of Na2MoO4·2H2O was dissolved into 10 mL of deionized water at room temperature. Then, the Se solution was slowly dropwise added into the Na2MoO4·2H2O solution at room temperature and the resulting homogeneous solution were then transferred into a 25 ml Teflon-lined stainless-steel autoclave. After that, a piece of pretreated Ni foam (2 cm × 2 cm, ~0.16 g) was immersed into the mixed solution. The autoclave was sealed and maintained at 200 oC for 24 h. After cooling to room temperature naturally, the sample was thoroughly rinsed with deionized water and ethanol, and finally dried in a vacuum oven at 60 oC. For comparison purpose, NiSe and MoSe2 were also prepared under the same process with the equivalent of Se precursor but without adding Na2MoO4·2H2O or Ni foam, respectively. The other preparation conditions are the same as that of the NiSe@MoSe2 nanosheet arrays. Preparation of nitrogen-doped pomelo mesocarps-based carbon nanosheet (N-PMCN) The N-PMCN was synthesized according to our previous reported work with slightly modifications.29 Briefly, 2.0 g of the pretreated pomelo mesocarps, 2.0 g of urea and 2.0 g of CaCl2 were mixed in 30 mL ethanol solution, and then evaporated the solvent in an air dry oven at 80 oC to form solid block carbon precursor mixtures. Finally, the as-obtained carbon precursor was activated and carbonized at 800 oC for 2 h at a heating rate of 5 oC min-1 in a slow N2 flow. The resulting sample was then repeatedly stirred washed with 2 M HCl to remove the inorganic salts, and then the sample was filtered and thoroughly washed by distilled water and dried in an oven at 60 oC.

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RESULTS AND DISCUSSION Characterizations of NiSe@MoSe2 nanosheet arrays positive electrode materials The novel NiSe@MoSe2 nanosheet arrays are designed and prepared via a simultaneous one-step hydrothermal growth method using nickel foam as nickel precursor and nucleation framework, selenium powder as Se precursor in presence of sodium molybdate solution. The fabrication process of the NiSe@MoSe2 heterostructures is schematically illustrated in Figure 1. The NiSe@MoSe2 heterostructures are designed based on the following considerations: (1) the nickel foam can work as nickel precursor for the synthesis of NiSe and as a support nucleation framework for the crystal growth of MoSe2 nanosheets; (2) NiSe and MoSe2 can be simultaneously formed and grew in the same reaction system, promoting the formation of the stable and integrated heterostructures; (3) the MoSe2 nanosheets grew and integrated on the surface of NiSe support matrix to form the unique NiSe@MoSe2 heterostructures.

Figure 1 Schematic illustration of the formation of NiSe@MoSe2 nanosheet arrays. The crystalline phases of the as-prepared NiSe, MoSe2 and NiSe@MoSe2 nanosheet arrays were first investigated by X-ray diffraction (XRD), as shown in Figure 2a. By comparing the XRD pattern of NiSe and standard pattern reference data, all of the diffraction peaks in NiSe matrix can be indexed to the hexagonal NiSe (JCPDS card no. 65-9451). For MoSe2 material, the diffraction peaks at 2θ=12.7o, 31.9o, 38.2o and 56.4o, corresponding to the hexagonal MoSe2 (JCPDS card no. 87-2419) for the (002), (100), (103) and (110) planes, respectively. For the characteristic reflections from 7



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NiSe@MoSe2, the strong diffraction peaks of NiSe at 2θ=32.7o, 43.9o, 49.5o, 58.9o and 60.6o, corresponding to the (101), (102), (110), (103) and (201) planes, respectively, also can be observed. However, we could just observe the weak diffraction peak reflections of MoSe2 in the NiSe@MoSe2 heterostructures, which may be due to the relatively low crystallinity and the reduced size of the crystallites in different dimensions of MoSe2.30 In addition to the diffraction peak reflections of NiSe and MoSe2 in the NiSe@MoSe2, there is no extra peak of impurity can be detected, which can confirme that the NiSe@MoSe2 heterostructures are only composed of NiSe and MoSe2 nanomaterials. The morphologies of the samples were characterized by field emission scanning electron microscopy (FE-SEM). As shown in Figure 2b, the as-grown NiSe shows lumpy surface with many irregular trigonal pyramidal blocks. One can see that the as-synthesized MoSe2 (Figure 2c) exhibits a flowerlike architecture with intertwined nanosheet-like subunits. More interestingly, it is obvious that the NiSe@MoSe2 heterostructures (Figure 2d-e) show the large-area and uniform aligned ultrathin nanosheets with intertwined structure. Furthermore, the cross-sectional SEM image of asgrown NiSe@MoSe2 further observed the homogeneous vertical nanosheet arrays structure (Figure 2f). In particular, the uniform vertical MoSe2 nanosheet arrays are almost fully covered and anchored on the NiSe support matrix to form integrated NiSe@MoSe2 heterostructures. Even upon repeated washing and ultrasound processing, the MoSe2 nanosheet arrays are well-anchored on the NiSe support matrix, suggesting the strong combination between MoSe2 and NiSe, which may be due to the good compatibility and matchability between the crystal structure of hexagonal NiSe and MoSe2 since they have the same space group.23 The results also reveal that the nickel foam or nickel compounds framework can directly and effectively induced the growth of MoSe2 nanosheet arrays, and ultimately form a unique core-shell structure of NiSe@MoSe2 nanosheet arrays. Such novel heterostructure architecture is a feasible way to prevent the aggregation of MoSe2 nanosheets and

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potentially increase the electronic or ion transport path to facilitate the electron transfer between the nanosheet edges and the conductive substrate.

Figure 2 (a) XRD patterns of the NiSe, MoSe2 and NiSe@MoSe2 samples; FE-SEM images of (b) NiSe; (c) MoSe2 and (d-e) NiSe@MoSe2 nanosheet arrays; (f) the cross-section image of NiSe@MoSe2 nanosheet arrays.

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Figure 3 (a-b) TEM images of the MoSe2 nanosheet from the NiSe@MoSe2 nanosheet arrays; (c) Element mapping images of NiSe@MoSe2 nanosheet arrays; (d) EDS spectrum of NiSe@MoSe2 nanosheet arrays; (e-g) The distribution images of various elements of NiSe@MoSe2 nanosheet arrays (selected from the square region of Figure 3c). The transmission electron microscopy (TEM) was further employed to investigate the structure of NiSe@MoSe2 nanosheet arrays, the results as shown in Figure 3a-b. The TEM images clearly show

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the intertwined and highly interconnected network morphology of the MoSe2 nanosheet from the NiSe@MoSe2 nanosheet arrays. The obvious folded nanosheet layers indicate the ultrathin nature of the as-grown MoSe2 nanosheets. Some parallel folded textures of MoSe2 can be observed in the high-resolution TEM (HRTEM) image (Figure 3b), corresponding to the layers of MoSe2 nanosheets. Furthermore, the interplanar distance of 0.68 nm is distinctly observed (inset in Figure 3b), which agrees well with the (002) plane of hexagonal MoSe2. In order to further understand the heterostructure composition of NiSe@MoSe2 nanosheet arrays, the energy-dispersive X-ray spectroscopy (EDS) elemental mapping was conducted to reveal the actual elements distribution between the MoSe2 nanosheets and NiSe matrix (Figure 3c-g). The corresponding EDS color maps results confirm the composition of NiSe@MoSe2 nanosheet arrays are mainly consist of Ni, Se and Mo elements (Figure 3d). The cross-section SEM image (Figure 3c) and corresponding EDS elemental mapping (in the square region of Figure 3c) analyses also reveal the homogeneous distribution of Ni and Se elements in the matrix of NiSe@MoSe2, while Mo and Se elements are mainly distributed in the matrix surface of NiSe@MoSe2 (Figure 3e-g). The results further confirmed that the MoSe2 nanosheets and NiSe matrix are grown simultaneously from nickel foam framework. The surface chemical bonding state and compositions of the NiSe@MoSe2 nanosheet arrays are further characterized by the X-ray photoelectron spectroscopy (XPS), as shown in Figure S1 in Supporting Information (SI). The characteristic peaks of Ni, Mo and Se elements were observed in the survey scan spectrum (Figure S1a). The high resolution spectra of Mo 3d, Ni 2p, and Se 3d are used to determine their oxidation states. The high resolution XPS spectra of Ni 2p (Figure S1b) showed two major peaks at the binding energy values of 852.4 and 869.8 eV which belong to the spin-orbit splitting of Ni 2p3/2 and Ni 2p1/2 levels, respectively. These two spin-orbit splittings near the Ni 2p3/2 and Ni 2p1/2, along with both two shake-up satellites, designate that the Ni species were in +2 oxidation state.31 The high resolution XPS spectra of Mo 3d (Figure S1c) showed two peaks located at 226.5 and 229.8 eV arise from Mo-Se structures, which can be assigned to the Mo 3d5/2

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and Mo 3d3/2 of Mo (IV). In addition, the binding energy value of 234.1 eV is originated from Mo 3d3/2 of Mo (VI) components, which maybe related with the defects in MoSe2, for example of Mo-O phase.32 Furthermore, the binding energy values of 52.1 eV and 53.2 eV are assigned to Se 3d5/2 and Se 3d3/2, respectively, while the binding energy value of 56.9 eV is ascribed to the oxidized Se (Figure S1d).32 The electrochemical behaviors of NiSe@MoSe2 nanosheet arrays were first performed under the three-electrode system by cyclic voltammograme (CV) and galvanostatic charge/discharge (GCD) in a 2 M KOH aqueous electrolyte. The hydrophilic carbon cloth was used as current collectors to prepare the working electrodes (Figure S2b, Supporting Information). Figure 4a shows the typical CV curves of as-synthesized MoSe2, NiSe and NiSe@MoSe2 nanosheet arrays at a scan rate of 30 mV s-1 in the operating voltage of -0.1~0.65 V (vs Hg/HgO). The CV curve of the carbon cloth shows a horizontal straight line, indicating it possesses a negligible capacitance. By comparison, the CV curve of the pure MoSe2 shows a near-rectangular curve shape with small electrochemical active area and without any obvious redox peaks at fast scan rate, which indicates that the pristine MoSe2 possesses a limited capacity. The result is similar to the electrochemical behavior of MoS2, because both MoSe2 and MoS2 belong to the transition metal chalcogenides and S and Se elements are in same primary family, thus they have similar properties.19,32 The NiSe electrode exhibits a pair of redox peaks, indicating a typical battery-type Faradaic behavior. The corresponding reversible redox reaction could be expressed as follows:25 NiSe + OH- ↔ NiSeOH + e-

(1)

Compared to that of pristine NiSe, it can be found that the CV curve of NiSe@MoSe2 nanosheet arrays electrode is similar to the NiSe electrode but shows greater electrochemical active area, indicating the much higher faradaic redox reactions and larger capacity in the NiSe@MoSe2 nanosheet arrays. In addition, the oxidized and reductive peaks of NiSe@MoSe2 nanosheet arrays are shifted slightly to higher and lower potentials than that of NiSe electrode, respectively, which are

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likely due to the lower conductivity of the NiSe@MoSe2 nanosheet arrays than the pristine NiSe matrix, lead to the low redox reversible processes.33 Figure 4b shows the CV curves of NiSe@MoSe2 electrode at different scan rates. With increase of the scan rates from 10 mV s-1 to 50 mV s-1, the CV curves area and the peak current obviously increase and the pair of redox peaks are still observed clearly. These results suggest that the NiSe@MoSe2 electrode exhibits rapid and reversible Faradic behavior and high rate ability.

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Figure 4 (a) CV curves of MoSe2, NiSe and NiSe@MoSe2 in 2 M KOH electrolyte; (b) CV curves of NiSe@MoSe2 at different scan rates; (c) GCD curves of NiSe@MoSe2 at different current densities; (d) Specific capacities of different electrodes at different current densities; (e) Nyquist plots of the NiSe, MoSe2 and NiSe@MoSe2 electrodes; (f) Cycling stability of the NiSe, MoSe2 and NiSe@MoSe2 electrodes at 5 A g-1. The GCD curves of the NiSe@MoSe2 nanosheet arrays electrode were collected between 0 and 0.6 V (vs Hg/HgO) at various specific current densities from 1 to 15 A g-1 ( Figure 4c). The charge curves are almost symmetrical to their discharge curves and possess a couple of charging and discharging platform which corresponding to the reflection of oxidation and reduction process, respectively, indicating typical redox reactions of the material and these results were consistent with the electrochemical behavior of CV curves. The corresponding discharge capacities at various current densities were calculated from GCD curves (Figure 4c), and the results are shown in Figure 4d. Encouragingly, the NiSe@MoSe2 nanosheet arrays electrode exhibits excellent specific capacity of 128.2 mA h g-1 at current densities of 1 A g-1, which is much higher than those of the NiSe (85.2 mAh g-1) and MoSe2 (20.7 mAh g-1) counterparts under the same current density. With the increase of the current densities from 1 to 15 A g-1, the NiSe@MoSe2 electrode can still maintain a specific capacity as high as 97.8 mAh g-1, which is about 76% capacity retention and its value is also comparable to the NiSe matrix electrode (59%). The electrochemical impedance spectroscopy (EIS) spectra of the NiSe, MoSe2 and NiSe@MoSe2 electrodes are depicted in Figure 4e. It could be observed obviously that the NiSe electrode exhibited a smaller charge transfer resistance (Rct) than the MoSe2 and NiSe@MoSe2 electrodes. However, the Rct of the NiSe@MoSe2 electrode is obviously lower than that of MoSe2 electrodes. These results further indicate that the NiSe not only acts as the framework for growing MoSe2 nanosheets but also improves the electrical conductivities of the NiSe@MoSe2 nanosheet arrays resulting in fast electron transport from the NiSe matrix to the MoSe2 nanosheets. Moreover, the NiSe@MoSe2 nanosheet

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arrays electrode possesses about 93.7% specific capacity retention after 1000 cycles at a current density of 5 A g-1 (Figure 4f), whose cycling stability is significantly better than that of the NiSe electrode (72.9%). The result further confirms that the NiSe@MoSe2 nanosheet arrays with the aligned ultrathin nanosheets can facilitate electrolyte ions diffusion and effectively buffer the volume change during the charge/discharge processes. Table S1 summarizes the electrochemical performance of the NiSe@MoSe2 nanosheet arrays and the typical metal chalcogenides electrodes for supercapacitors. The above results reveal that NiSe@MoSe2 nanosheet arrays exhibit high specific capacity, high rate capability and excellent cycling stability. The much enhanced electrochemical properties of assynthesized NiSe@MoSe2 material could be attributed largely to the following factors: (i) the unique vertical nanosheet arrays structure can prevent the aggregation of MoSe2 nanosheets and provide a path for the ions insertion/extraction within the NiSe matrix, which may offer a large number of exposed reaction active sites and transportation channels, improving the specific capacity significantly.22 (ii) The rich voids pace between interlaced MoSe2 nanosheets arrays provide an open space for easy electrolyte diffusion and can also serve as an “electrolyte reservoir” to promote the transport of electrolyte ions during charge/discharge process, resulting in high rate capability. Therefore, constructing the NiSe@MoSe2 heterostructures is promising for the creation of alternative positive electrode material for supercapacitors. Characterizations of N-PMCN negative electrode materials The nitrogen-doped pomelo mesocarps-based carbon nanosheet (N-PMCN) is prepared by simultaneous CaCl2 activation and urea nitrogen-doped treatment using green bio-waste (pomelo mesocarps) as carbon precursor. The N-PMCN was designed according to the following considerations: (i) The pomelo mesocarp is mainly composed of lignin and cellulose, which highly cross-linked cellulosic fibrils network is a desirable precursor to forming interconnected porous carbon nanomaterials; (ii) CaCl2 has strong ammonia adsorption ability,40 which can cause volume

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expansion during the adsorption process. Therefore, the CaCl2 can be used to immobilize ammonia which generated through urea pyrolysis in the activated carbon precursor process, leading to high nitrogen doping content in carbon skeletons; and (iii) the urea also can play the dual role of nitrogen source and expansion agent in the whole system,35 thus induce formation of porous carbon nanosheets structure. Therefore, we expect the as-prepared N-PMCN material to show favorable features such as large surface area, porous architecture and high nitrogen contents as potential negative electrode for supercapacitors. The SEM and TEM were employed to investigate the morphology and microstructures of the NPMCN, the results as shown in Figure 5. The N-PMCN exhibits an interconnected sheet-like structure with many irregular voids, which is revealed by typical SEM images (Figure 5a). Moreover, a lot of soft wrinkles in the edges of N-PMCN nanosheets are clearly visible by high magnification SEM (Figure 5b), which ought to be derived from the ultrathin carbon walls consist of several layers of graphene nanosheets.36 The highly interconnected and corrugated ultrathin carbon nanosheet was further confirmed by TEM (Figure 5c). No lattice fringe can be observed in the HRTEM image (Figure 5d), revealing the disordered amorphous carbon structure of the N-PMCN material. These results also demonstrate that the carbon material with crumpled and interconnected nanosheet structure can be fabricated by the combination of chemical activation and gas expansion method.37 The pore-size characterization of the N-PMCN was performed by measuring the nitrogen adsorption/desorption techniques. The isotherm and corresponding pore size distribution curve of the N-PMCN are shown in Figure 5e and Figure 5f, respectively. It shows a type-IV isotherm with obvious hysteresis loops in the relative pressure of ca. 0.50-0.99 P/P0, especially at high relative pressure (P/P0 > 0.90), suggesting the presence of mesoporous and macroporous structures. The noteworthy macroporous structure in N-PMCN may be a reflection of the irregular voids caused by intertwined carbon nanosheets. Besides, the adsorbed volume of N-PMCN is steep increase at low pressures (P/P0 < 0.40), implying the presence of a certain microporosity. The specific surface area

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and pore volume of the N-PMCN material measured by the Brunauer-Emmett-Teller (BET) method are 1163 m2 g-1 and 0.82 cm3 g-1, respectively. The corresponding pore size distribution curve of NPMCN is calculated by the Barrett-Joyner-Halenda (BJH) method, which shows a high N2 sorption pore volume in the small pore width range and the pore size distribution mainly centered in the range of 2-4 nm, signifying the presence of superior mesoporous structures in N-PMCN material.

Figure 5 (a-b) FE-SEM images of N-PMCN; (c-d) TEM images of N-PMCN; (e) Nitrogen adsorption-desorption isotherms of the N-PMCN; (f) the pore size distribution of the N-PMCN.

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The typical XRD pattern of N-PMCN in Figure 6a shows a typical broad (002) diffraction peak at 2θ = 21.8o, and the corresponding interlayer spacing (0.40 nm) is slightly larger than the natural graphite value (0.34 nm). The results indicated that there are regions of expanded stacking for example through corrugated or disordered carbon layers.38 The Raman spectrum (Figure 6b) of the N-PMCN shows the typical D-band (about 1348 cm-1) and G-band (about 1601 cm-1) peaks, which are closely related to the disordered graphitic carbon and the graphite sp2 in-plane carbon phase, respectively.39 One can see that the N-PMCN exhibits a relatively stronger G-band signal than Dband, and their intensity ratio (ID/IG) is calculated to be 0.94, demonstrating the interconnected NPMCN is mainly made of pyrolytic turbostratic carbon structure with some ordered graphitic feature.34 The surface element of the N-PMCN was further verified by X-ray photoelectron spectroscopy (XPS), as shown in Figure 6c. The peaks located at around 284.4, 400.1 and 532.1 eV are corresponding to the C1s, N1s and O1s spectrum, respectively. Specifically, four types of nitrogen bonding configurations are confirmed by high-resolution XPS (Figure 6d). The peaks at 398.4, 400.6, 401.5 and 402.7 eV can be identified to correspond to pyridinic-N (N-6), pyrrolic-N (N-5), quaternary-N (N-Q), and pyridine-N-oxide (N-X), respectively.29 In addition, the test results of elemental analysis display the nitrogen content in N-PMCN is 9.07 wt%. These results demonstrate that the incorporate with CaCl2 activation and urea gasification expansion methods can obtain the carbon materials with unique ultrathin nanosheet structure and large surface area as well as effective nitrogen doping in carbon skeletons. Thus, it can be assumed that the as-prepared NPMCN as electrode material for supercapacitor can not only increase the surface wettability and provide an additional capacity of carbon electrode material owing to high nitrogen doping content,28 but also shorten the ion diffusion paths and improve the ion buffer storage spaces due to the interconnected porous nanosheet structure. Therefore, the as-prepared N-PMCN can be used as potential negative electrode for supercapacitor applications.

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Figure 6 (a) XRD pattern and (b) Raman spectrum of N-PMCN material; (c) XPS spectrum of NPMCN; (d) N1s XPS spectra of N-PMCN. The electrochemical tests of the N-PMCN electrode material was also performed in a threeelectrode system using 2 M KOH aqueous electrolyte. For the purpose of comparison, the commercial activated carbon (AC) was also evaluated as electrode material under the same test conditions. Figure 7a shows the typical CV curves of the N-PMCN and AC electrode materials at a scan rate of 50 mV s-1 within a potential range of -1.0~0 V (vs. Hg/HgO). The two curves exhibit a similar rectangular shape, which implies that the electrode materials show an ideal capacitive behavior. Obviously, the area surrounded by the CV curve of N-PMCN is larger than that of the studied AC sample, suggesting the high capacitance. In addition, the CV curves of N-PMCN still maintain a stable rectangular-like shape at the scan rate as high as 150 mV s-1 (Figure 7b), indicating the N-PMCN electrode exhibits a remarkable rate capability. 19



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Figure 7 (a) CV curves of AC and N-PMCN electrodes in 2 M KOH electrolyte; (b) CV curves of NPMCN at different scan rates; (c) GCD curves of N-PMCN at different current densities; (d) Specific capacitances of AC and N-PMCN at different current densities. The GCD measurements of N-PMCN electrode material were carried out at various current densities (0.5 to 15 A g-1) in the operating voltage from -1.0 to 0 V, as shown in Figure 7c. All the charging and discharging curves are highly symmetric under different current densities, implying the electrode possess highly reversible charge and discharge behaviors. The gravimetric specific capacitance of the materials was calculated from the discharge portion of the GCD profiles according to the equation (Electrochemical measurements section, Supporting Information) and the corresponding results as shown in the Figure 7d. As can be noticed, the N-PMCN electrode exhibits a very high specific capacitance of 223 F g-1 at 1 A g-1, which is 1.6-fold larger than the AC electrode under the same current density. With the increase of the discharge current densities from 0.5 to 15 A g-1, the N-PMCN electrode can still preserve a high specific capacitance of 178 F g-1, which is about 20


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77% capacitance retention and the value is significantly higher than that of the typical electric double-layer capacitive AC electrode material (66%). Therefore, the above results clearly reveal that the high specific capacitance and excellent rate capability of as-prepared N-PMCN are attributed to the unique porous nanosheet structure and high nitrogen doping, which will shorten the ion diffusion paths, improve the ion buffer storage spaces and provide effective capacitance. Electrochemical behavior of the as-assembled asymmetric supercapacitor Considering the excellent electrochemical performances of NiSe@MoSe2 and N-PMCN electrodes with complementary operating voltage in the same KOH aqueous electrolyte, a novel asymmetric supercapacitor (ASC) was assembled based on these materials used as the positive and negative electrodes, respectively. The schematic illustration of the NiSe@MoSe2//N-PMCN ASC device is shown in Figure 8a. To further investigate the stable potential windows of NiSe@MoSe2 and NPMCN prior to the evaluation of the ASC device, these two electrode materials was first performed CV tested in a three-electrode cell. As shown in Figure 8b, the N-PMCN electrode and NiSe@MoSe2 electrode were measured within a potential window of -1.0~0 V and -0.1 to 0.65 V (vs. Hg/HgO) at a scan rate of 30 mV s-1 in 2 M KOH solution, respectively. Therefore, the total operating device voltage can be expressed as the sum of the potential range of the positive and negative electrodes, and it can be achieve a working voltage of 1.65 V when they are assembled into the ASC device. To construct the ASC, the loading mass ratio of electroactive materials (NiSe@MoSe2/N-PMCN) was estimated to be 0.58 according to the charge balance relationship (see two-electrode fabrication section, Supplementary Information). In order to ensure electrochemical stability and the practical available operating voltage of the asfabricated ASC device, it was firstly evaluated at various voltage windows from 1.2 to 1.8 V (Figure S3, Supporting Information). As expected, the NiSe@MoSe2//N-PMCN ASC device exhibits an ideal capacitive behavior with a stable CV curves even at the voltage window up to 1.65 V. However, the current value increases sharply in high potential when the potential window continued to extend

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to 1.8 V, which probably originated from the electrolyte decomposition by oxygen evolution.41 Therefore, to ensure the stability and electrochemical reversibility of the ASC device, the operating voltage was determined to be 1.65 V for subsequent electrochemical performance tests.

Figure 8 (a) Schematic illustration of the NiSe@MoSe2//N-PMCN ASC; (b) Comparative CV curves of NiSe@MoSe2 nanosheet arrays and N-PMCN at 30 mV s-1 in three-electrode cell; (c) CV curves of NiSe@MoSe2//N-PMCN ASC at different scan rates; (d) GCD curves NiSe@MoSe2//NPMCN ASC at various current densities; (e) Ragone plots of the NiSe@MoSe2//N-PMCN, 22


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NiSe@MoSe2//AC ASC devices and previously reported metal chalcogenide based ASC devices42-46; (f) Cycling performance of the NiSe@MoSe2//N-PMCN ASC device. In Figure 8c, the CV curves of NiSe@MoSe2//N-PMCN ASC device measured at different scan rates from 10 to 100 mV s-1 with operating voltage of 1.65 V exhibit distorted semi-rectangular shapes, which may be attributed to the contribution from the typical faradaic positive electrode (Figure 8b). Moreover, the original rectangular-like shapes and with typical redox peaks are also observed from the CV curves even at high scan rates, indicating outstanding reversible battery-type faradaic behavior. The GCD curves of the NiSe@MoSe2//N-PMCN ASC device was recorded at different current densities with an operating voltage of 0-1.65 V. As shown in Figure 8d, the ASC device shows good capacitive properties based on its reasonably symmetric charge and discharge curves. For the purpose of comparison, we also fabricated the NiSe@MoSe2//AC ASC device based on NiSe@MoSe2 and AC as positive and negative electrodes, respectively, and evaluate its electrochemical performance (Figure S4, Supporting Information). The Ragone plots of the NiSe@MoSe2//N-PMCN and NiSe@MoSe2//AC ASC devices are obtained based on their GCD datas, as shown in Figure 8e. The NiSe@MoSe2//N-PMCN ASC device exhibits a high energy density of 32.6 Wh kg-1 at a power density of 415 W kg-1 and can be maintain 19.6 Wh kg-1 at a high power density of 8592 W kg-1. However, the NiSe@MoSe2//AC ASC device exhibits the maximum energy density of 24.5 Wh kg-1 at power density of 400 W kg-1 and just retain about 11.1 Wh kg-1 at power density of 7986 W kg-1. The energy density of NiSe@MoSe2//N-PMCN ASC device is much higher than that of NiSe@MoSe2//AC ASC device, which results could be attributed to the excellent electrochemical performances of NiSe@MoSe2 and N-PMCN electrodes. Meanwhile, the results also demonstrate that the use of the N-PMCN as negative electrode can significantly improve the performance of the ACS device. Furthermore, the maximum energy density of NiSe@MoSe2//NPMCN ASC device is also comparable to the many previously reported aqueous ASC devices based

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on metal compounds as positive electrodes and carbon materials as negative electrodes (Table S2, Supporting Information). The EIS test was also conducted to further insight into the advantages of the NiSe@MoSe2//NPMCN ASC device. The EIS spectra and the corresponding simulated equivalent circuit of the asfabricated ASC device are shown in Figure S5 (Supporting Information). In the low frequency region, the near-vertical slopes indicate the device possesses a typical capacitive behavior and fast electrolyte ions diffusion process,47 which should be attribute to the interconnected hierarchical porous structures of the electrodes as our above deductive results. In the high frequency area, the asfabricated ASC device exhibited low bulk resistance (Rs=0.72 Ω) and low charge-transfer resistance (Rct=1.36 Ω), which resistance values are obtained and calculated from the intercept of the real axis Z' and the diameter of the resistor-capacitor loop, respectively. The cycling durability of the ACS device is further evaluated at a current density of 5 A g-1 and shows high capacitance retention of 91.4% achieved after 5000 cycles, revealing its excellent long-term cyclic stability (Figure 8f). It can be found that the specific capacitance of ASC device is increases distinctly in the initial 200 cycles, which may be caused by the improve wettability of electrode materials during the charge/discharge process. The small charge-transfer resistance and excellent cycling stability of the NiSe@MoSe2//NPMCN ASC device could be attributed to the original vertical nanosheet arrays architecture of NiSe@MoSe2 and the porous nanosheet structure of N-PMCN. Their interconnected hierarchical porous structures provide rich open voids for the fast electrolyte ion diffusion and effective electron transfer, and also serve as an “electrolyte reservoir” to buffer the volume change of core/shell heterostructure of NiSe@MoSe2 during the charge/discharge process. The demo experiment of two tandems NiSe@MoSe2//N-PMCN ASC devices lighting up the red light-emitting diode (LED, 5 mm diameter) and lasting for about 6 minutes easily when charged the devices to 3.3 V within only 5 seconds (inset in Figure 8f), demonstrating a great potential for high power and high energy storage applications.

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CONCLUSIONS In summary, a novel NiSe@MoSe2 positive electrode with uniform vertical nanosheet arrays architecture and considerable specific capacity is designed and prepared by a facile one-step hydrothermal growth method, in which nickel foam as nickel precursor and nucleation framework. Besides, the porous interconnected N-PMCN negative electrode with high nitrogen doping level (~9 wt%) and high specific capacitance is prepared via simultaneous chemical activation and urea nitrogen-doped method. Based on the unique architecture and outstanding electrochemical performance of NiSe@MoSe2 nanosheet arrays and N-PMCN electrodes, a novel NiSe@MoSe2//NPMCN ASC device with a maximum operating voltage of 1.65 V was constructed and showed a high energy density and power density (32.6 Wh kg-1 at a power density of 415 W kg-1) as well as outstanding cycling stability. These results indicate their potentials to work as promising candidate materials for high-performance energy storage application. The work presented here not only suggests the possibility to construct the stable heterostructures into promising electrode materials, but also presents a way to fabricate novel asymmetric supercapacitor devices based on highperformance faradaic electrode materials and low cost biomass-based carbon materials.

ASSOCIATED CONTENT Supporting Information Electrode fabrication, electrochemical measurements, calculation methods, Figure S1-S5 and Table S1-S2. This information is available free of charge via the Internet at http://pubs.acs.org/. AUTHOR INFORMATION Corresponding Author *E-mail: [email protected] (G. Ma); [email protected] (Z. Lei) Notes

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The authors declare no competing financial interest. ACKNOWLEDGMENT This work was supported by the National Science Foundation of China (21664012, 51462032), the program for Changjiang Scholars and Innovative Research Team in University (IRT15R56), the Innovation Team Basic Scientific Research Project of Gansu Province (1606RJIA324). H. Peng would like to acknowledge the China Scholarship Council for the Joint Ph. D. program.

REFERENCES (1) Wang, G.; Zhang, L.; Zhang, J. A Review of Electrode Materials for Electrochemical Supercapacitors. Chem. Soc. Rev. 2012, 41, 797-828. (2) Zhu, Y.; Murali, S.; Stoller, M. D.; Ganesh, K. J.; Cai, W.; Ferreira, P. J.; Pirkle, A.; Wallace, R. M.; Cychosz, K. A.; Thommes, M.; Su, D.; Stach, E. A.; Ruoff, R. S. Carbon-Based Supercapacitors Produced by Activation of Graphene. Science 2011, 332, 1537-1541. (3) Salanne, M.; Rotenberg, B.; Naoi, K.; Kaneko, K.; Taberna, P. L.; Grey, C. P.; Dunn, B.; Simon, P. Efficient Storage Mechanisms for Building Better Supercapacitors. Nat. Energy 2016, 1, 16070. (4) Veeramani, V.; Madhu, R.; Chen, S. M.; Sivakumar, M. Flower-Like Nickel–Cobalt Oxide Decorated Dopamine-Derived Carbon Nanocomposite for High Performance Supercapacitor Applications. ACS Sustainable Chem. Eng., 2016, 4, 5013-5020. (5) Yan, J.; Wang, Q.; Wei, T.; Fan, Z. Recent Advances in Design and Fabrication of Electrochemical Supercapacitors with High Energy Densities. Adv. Energy Mater. 2014, 4. (6) Peng, H.; Ma, G.; Mu, J.; Sun, K.; Lei, Z. Low-Cost and High Energy Density Asymmetric Supercapacitors Based on Polyaniline Nanotubes and MoO3 Nanobelts. J. Mater. Chem. A 2014, 2, 10384-10388.

26


Page 26 of 32

Page 27 of 32

1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60


(7) Liu, S.; Sun, S.; You, X. Z. Inorganic Nanostructured Materials for High Performance Electrochemical Supercapacitors. Nanoscale 2014, 6, 2037-2045. (8) Chen, H.; Zhou, M.; Wang, T.; Li, F.; Zhang, Y. Construction of Unique Cupric OxideManganese Dioxide Core-Shell Arrays on a Copper Grid for High-Performance Supercapacitors. J. Mater. Chem. A 2016, 4, 10786-10793. (9) Huang, M.; Li, F.; Dong, F.; Zhang, Y.; Zhang, L. MnO2-Based Nanostructures for HighPerformance Supercapacitors. J. Mater. Chem. A 2015, 3, 21380-21423. (10) Zhong, C.; Deng, Y.; Hu, W.; Qiao, J.; Zhang, L.; Zhang, J. A Review of Electrolyte Materials and Compositions for Electrochemical Supercapacitors. Chem. Soc. Rev. 2015, 44, 7484-7539. (11) Dubal, D. P.; Ayyad, O.; Ruiz, V.; Gómez-Romero, P. Hybrid Energy Storage: The Merging of Battery and Supercapacitor Chemistries. Chem. Soc. Rev. 2015, 44, 1777-1790. (12) Wang, X.; Yan, C.; Yan, J.; Sumboja, A.; Lee, P. S. Orthorhombic Niobium Oxide Nanowires for Next Generation Hybrid Supercapacitor Device. Nano Energy 2015, 11, 765-772. (13) Zhu, S.; Jia, J.; Wang, T.; Zhao, D.; Yang, J.; Dong, F.; Shang, Z.; Zhang, Y. Rational Design of Octahedron and Nanowire CeO2@MnO2 Core-Shell Heterostructures with Outstanding Rate Capability for Asymmetric Supercapacitors. Chem. Comm. 2015, 51, 14840-14843. (14) Zhu, S.; Zhang, J.; Ma, J.; Zhang, Y.; Yao, K. Rational Design of Coaxial Mesoporous Birnessite Manganese Dioxide/Amorphous-Carbon Nanotubes Arrays for Advanced Asymmetric Supercapacitors. J. Power Sources 2015, 278, 555-561. (15) Lim, E.; Jo, C.; Kim, M. S.; Kim, M. H.; Chun, J.; Kim, H.; Park, J.; Roh, K. C.; Kang, K.; Yoon, S.; Lee, J. Hybrid Supercapacitors: High-Performance Sodium-Ion Hybrid Supercapacitor Based

on

Nb2O5@Carbon

Core-Shell Nanoparticles

and

Nanocomposites. Adv. Funct. Mater. 2016, 26, 3553.

27


Reduced

Graphene

Oxide


1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60

(16) Peng, H.; Ma, G.; Sun, K.; Zhang, Z.; Li, J.; Zhou, X.; Lei, Z. A Novel Aqueous Asymmetric Supercapacitor Based on Petal-Like Cobalt Selenide Nanosheets and Nitrogen-Doped Porous Carbon Networks Electrodes. J. Power Sources 2015, 297, 351-358. (17) Huang, X.; Zeng, Z.; Zhang, H. Metal Dichalcogenide Nanosheets: Preparation, Properties and Applications. Chem. Soc. Rev. 2013, 42, 1934-1946. (18) Tan, C.; Zhang, H. Two-Dimensional Transition Metal Dichalcogenide Nanosheet-Based Composites. Chem. Soc. Rev. 2015, 44, 2713-2731. (19) Ma, G.; Peng, H.; Mu, J.; Huang, H.; Zhou, X.; Lei, Z. In Situ Intercalative Polymerization of Pyrrole in Graphene Analogue of MoS2 as Advanced Electrode Material in Supercapacitor. J. Power Sources 2013, 229, 72-78. (20) Yu, X.; Yu, L.; Shen, L.; Song, X.; Chen, H.; Lou, X. W. D. General Formation of MS (M= Ni, Cu, Mn) Box-in-Box Hollow Structures with Enhanced Pseudocapacitive Properties. Adv. Funct. Mater. 2014, 24, 7440-7446. (21) Wang, X.; Liu, B.; Wang, Q.; Song, W.; Hou, X.; Chen, D.; Cheng, Y.; Shen, G. ThreeDimensional Hierarchical GeSe2 Nanostructures for High Performance Flexible All-Solid-State Supercapacitors. Adv. Mater. 2013, 25, 1479-1486. (22) Shen, J.; Wu, J.; Pei, L.; Rodrigues, M. T. F.; Zhang, Z.; Zhang, F.; Zhang, X.; Ajayan, P. M.; Ye, M. CoNi2S4-Graphene-2D-MoSe2 as An Advanced Electrode Material for Supercapacitors. Adv. Energy Mater. 2016, 6, 1600341. (23) Zhou, X.; Liu, Y.; Ju, H.; Pan, B.; Zhu, J.; Ding, T.; Wang, C.; Yang, Q. Design and Epitaxial Growth of MoSe2-NiSe Vertical Heteronanostructures with Electronic Modulation for Enhanced Hydrogen Evolution Reaction. Chem. Mater. 2016, 28, 1838-1846. (24) Gong, F.; Wang, H.; Xu, X.; Zhou, G.; Wang, Z. S. In Situ Growth of Co0.85Se and Ni0.85Se on Conductive Substrates as High-Performance Counter Electrodes for Dye-Sensitized Solar Cells. J. Am. Chem. Soc. 2012, 134, 10953-10958.

28


Page 28 of 32

Page 29 of 32

1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60


(25) Tang, C.; Pu, Z.; Liu, Q.; Asiri, A. M.; Sun, X.; Luo, Y.; He, Y. In Situ Growth of NiSe Nanowire Film on Nickel Foam as An Electrode for High-Performance Supercapacitors. ChemElectroChem 2015, 2, 1903-1907. (26) Jiang, H.; Lee, P. S.; Li, C. 3D Carbon Based Nanostructures for Advanced Supercapacitors. Energy Environ. Sci. 2013, 6, 41-53. (27) Dutta, S.; Bhaumik, A.; Wu, K. C. W. Hierarchically Porous Carbon Derived From Polymers and Biomass: Effect of Interconnected Pores on Energy Applications. Energy Environ. Sci. 2014, 7, 3574-3592. (28) Shen, W., Fan, W., Nitrogen-Containing Porous Carbons: Synthesis and Application. J. Mater. Chem. A 2013, 1, 999-1013. (29) Peng, H.; Ma, G.; Sun, K.; Zhang, Z.; Yang, Q.; Lei, Z. Nitrogen-Doped Interconnected Carbon Nanosheets From Pomelo Mesocarps for High Performance Supercapacitors. Electrochim. Acta 2016, 190, 862-871. (30) Zhou, X.; Jiang, J.; Ding, T.; Zhang, J.; Pan, B.; Zuo, J.; Yang, Q. Fast Colloidal Synthesis of Scalable Mo-Rich Hierarchical Ultrathin MoSe2-x Nanosheets for High-Performance Hydrogen Evolution. Nanoscale 2014, 6, 11046-11051. (31) Nagaraju, G.; Cha, S. M.; Sekhar, S. C.; Yu, J. S. Metallic Layered Polyester Fabric Enabled Nickel Selenide Nanostructures as Highly Conductive and Binderless Electrode with Superior Energy Storage Performance. Adv. Energy Mater. 2017, 7, 1601362. (32) Weng, Q.; Wang, X.; Wang, X.; Zhang, C.; Jiang, X.; Bando, Y.; Golberg, D. Supercapacitive Energy Storage Performance of Molybdenum Disulfide Nanosheets Wrapped with Microporous Carbons. J. Mater. Chem. A 2015, 3, 3097-3102. (33) Zhang, G.; Lou, X. W. D. General Solution Growth of Mesoporous NiCo2O4 Nanosheets on Various Conductive Substrates as High-Performance Electrodes for Supercapacitors. Adv. Mater. 2013, 25, 976-979.

29



1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60

(34) Tokarev, M. M.; Veselovskaya, J. V.; Yanagi, H.; Aristov, Y. I. Novel Ammonia Sorbents “Porous Matrix Modified by Active Salt” for Adsorptive Heat Transformation: 2. Calcium Chloride in ACF Felt. Appl. Therm. Eng. 2010, 30, 845-849. (35) Peng, H.; Ma, G.; Sun, K.; Zhang, Z.; Yang, Q; Ran, F.; Lei, Z. A Facile and Rapid Preparation of Highly Crumpled Nitrogen-Doped Graphene-Like Nanosheets for High-Performance Supercapacitors. J. Mater. Chem. A 2015, 3, 13210-13214. (36) Li, Y.; Li, Z.; Shen, P. K. Simultaneous Formation of Ultrahigh Surface Area and ThreeDimensional Hierarchical Porous Graphene-Like Networks for Fast and Highly Stable Supercapacitors. Adv. Mater. 2013, 25, 2474-2480. (37) Wakeland, S.; Martinez, R.; Grey, J. K.; Luhrs, C. C. Production of Graphene From Graphite Oxide Using Urea as Expansion-Reduction Agent. Carbon 2010, 48, 3463-3470. (38) Srinivas, G.; Zhu, Y.; Piner, R.; Skipper, N.; Ellerby, M.; Ruoff, R. S. Synthesis of GrapheneLike Nanosheets and Their Hydrogen Adsorption Capacity. Carbon 2010, 48, 630-635. (39) Huang, X.; Kim, S.; Heo, M. S.; Kim, J. E.; Suh, H.; Kim, I. Easy Synthesis of Hierarchical Carbon Spheres with Superior Capacitive Performance in Supercapacitors. Langmuir 2013, 29, 12266-12274. (40) Wollbrink, A.; Volgmann, K.; Koch, J.; Kanthasamy, K.; Tegenkamp, C.; Li, Y.; Richter, H.; Kämnitz, S.; Steinbach, F.; Feldhoff, A.; Caro, J. Amorphous, Turbostratic and Crystalline Carbon Membranes with Hydrogen Selectivity. Carbon 2016, 106, 93-105. (41) Ji, J.; Zhang, L.; Ji, H.; Li, Y.; Zhao, X.; Bai, X.; Fan, X.; Zhang, F.; Ruoff, R. S. Nanoporous Ni (OH)2 Thin Film on 3D Ultrathin-Graphite Foam for Asymmetric Supercapacitor. ACS Nano 2013, 7, 6237-6243. (42) Dai, C. S.; Chien, P. Y.; Lin, J. Y.; Chou, S. W.; Wu, W. K.; Li, P. H.; Wu, K. Y.; Lin, T. W. Hierarchically Structured Ni3S2/Carbon Nanotube Composites as High Performance Cathode Materials for Asymmetric Supercapacitors. ACS. Appl. Mater. Interfaces. 2013, 5, 12168-12174.

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Page 31 of 32

1 2 3 4 5 6 7 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 28 29 30 31 32 33 34 35 36 37 38 39 40 41 42 43 44 45 46 47 48 49 50 51 52 53 54 55 56 57 58 59 60


(43) Wu, Z.; Pu, X.; Ji, X.; Zhu, Y.; Jing, M.; Chen, Q.; Jiao, F. High Energy Density Asymmetric Supercapacitors from Mesoporous NiCo2S4 Nanosheets. Electrochim. Acta 2015, 174, 238-245. (44) Li, R.; Wang, S.; Wang, J.; Huang, Z. Ni3S2@CoS Core-Shell Nano-Triangular Pyramid Arrays on Ni Foam for High-Performance Supercapacitors. Phys. Chem. Chem. Phys. 2015, 17, 1643416442. (45) Guo, K.; Yang, F.; Cui, S.; Chen, W.; Mi, L. Controlled Synthesis of 3D Hierarchical NiSe Microspheres for High-Performance Supercapacitor Design. RSC Adv. 2016, 6, 46523-46530. (46) Chen, H.; Chen, S.; Fan, M.; Li, C.; Chen, D.; Tian, G.; Shu, K. Bimetallic Nickel Cobalt Selenides: A New Kind of Electroactive Material for High-Power Energy Storage. J. Mater. Chem. A 2015, 3, 23653-23659. (47) Lai, H.; Wu, Q.; Zhao, J.; Shang, L.; Li, H.; Che, R.; Lyu, Z.; Xiong, J.; Yang, L.; Wang, X.; Hu, Z. Mesostructured NiO/Ni Composites for High-Performance Electrochemical Energy Storage. Energy Environ. Sci. 2016, 9, 2053-2060.

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High-performance asymmetric supercapacitor designed with a novel NiSe@MoSe2 nanosheet arrays and nitrogen-doped carbon nanosheet Hui Peng,a Jiezi Zhou,a Kanjun Sun,b Guofu Ma*a, Zhiguo Zhang,a Enke Fenga and Ziqiang Lei*a

Synopsis High-performance asymmetric supercapacitor is assembled based on a novel NiSe@MoSe2 nanosheet arrays positive electrode and the nitrogen-doped pomelo mesocarps-based carbon nanosheet negative electrode.

Table of Contents Graphic

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High-Performance Asymmetric Supercapacitor Designed with a Novel

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