Introduction

With the rapid development of portable devices, green energy harvesting and electric automobiles, safe energy storage devices with improved power and energy densities are becoming increasingly important. Electrochemical devices are very promising energy storage devices, due to their short charging time, high power densities and long lifespans1,2. Among all these power sources, nanostructured electrode batteries and supercapacitors are the paradigm devices as they are promising to deliver power source with both high energy and power densities. The increasing applications of electrochemical devices in electronic devices and industries require on further improvement of the energy density, rate capability, safety and durability of electrodes, which to a large extent rely on the development of new electrode materials and novel electrode structures. Transition metal oxides (MOs such as RuO2, MnO2, NiO, CoO) and sulfides (MSs such as CoS, NiS, WS2 etc.) from an important group of electrode materials due to their abundant reversible redox reactions, high theoretical capacity and long cycle life3,4,5,6,7,8,9,10,11,12. Recently, the ternary cobalt nickel sulfides (NiCo2S4) has drawn great research interest because of their intriguing advantages over the binary MOs and MSs2,13,14. For instance, NiCo2S4 have an electrical conductivity of at least four orders of magnitude higher than that of either nickel oxides/sulfides or cobalt oxides/sulfides. High electrical conductivity could decrease the charge transfer resistance of the electrodes and thus leading to increased power density15,16. In addition, with the contributions from both nickel and cobalt ions, NiCo2S4 are expected to offer richer redox reactions than the binary sulfides and oxides and thus increased capacity.

Various NiCo2S4 nanostructures, including nanoparticles17,18, nanosheets19,20, nanotubes21 and microspheres22, have been synthesized. A common approach to apply these NiCo2S4 nanostructures as electrodes in electrochemical devices is to mix them with polymeric binder and carbon black and press the mixture onto current collectors. However, the use of conductive additive and binder inevitably increases the undesirable interparticle resistance which decreases the efficiency of electron transport among active materials23,24. Recently, it was shown that direct growth of NiCo2S4 nanowire arrays on metallic substrates could overcome the drawbacks from mixing active materials with conductive additive and binder and led to improved capacity and cyclic stability25,26. Though NiCo2S4 is important electrode material from those reported17,18,19,20,21,22, so far the change of electrochemical reactions on the surface/inside of NiCo2S4 materials has not been studied systematically. Compared with one dimensional (1D) nanostructure, three dimensional (3D) heterostructure will be able to more fully be present in the change of electrode materials during electrochemical reactions27,28,29. In this work, we synthesized for the first time a thin carbon layer coated three dimensional (3D) hierarchical NiCo2S4 core-shell nanowire arrays (NiCo2S4@C CSNAs) directly on graphene-coated Ni (Ni@G) foam. In comparison with the NiCo2S4 nanowire arrays on metallic substrates, the effective surface area of the active electrode materials was greatly increased and thus the electrochemical performances of the electrode was significantly improved, e.g., a high specific capacitance of 253 mAh g−1 at 3 A g−1, high rate capability of 163 mAh g−1 at 50 A g−1 (~64.4% of that at 3 A g−1) and long-term cycling stability with a capacity retention of 93.9% after 5000 cycles. We further studied comparatively the degradation mechanisms of hierarchical NiCo2S4 CSNAs electrodes with and without carbon coatings and revealed favorable roles of carbon coatings in maintaining the structural integrity and chemical composition of the hierarchical NiCo2S4 CSNAs during charge/discharge cycles.

Results

The hierarchical NiCo2S4 CSNAs were synthesized by hydrothermal method followed by sulfurization treatment (see the Supplementary Information I for Experimental details). Ni@G foams were used as substrates (Figure S1) and graphene was pre-coated on Ni foam to protect it which would otherwise become fragile during the sulfurization. For the synthesis of hierarchical NiCo2S4 CSNAs, the Ni@G foam was first immersed into an aqueous solution containing Ni2+, Co2+ and urea and the (Ni, Co) hydroxide nanowire arrays were grown uniformly on the surface of Ni@G foam, as shown in Figure S2. Then, the (Ni, Co) hydroxide precursor nanowire arrays were converted to highly-ordered hierarchical NiCo2S4 CSNAs via a facile sulfurization. Finally, the samples were annealed at 320 oC in Ar gas to get crystallized NiCo2S4 CSNAs. As shown in Fig. 1a, the NiCo2S4 nanowires on Ni@G foam possessed an average diameter of ~70 nm and length up to ~6 μm and their surfaces were relatively smooth after sulfurization for 12 h. After sulfurization for 24 h, the NiCo2S4 nanowires still remained the array structure, but the surface of nanowires became rough, as shown in Fig. 1b. Enlarged SEM image (inset in Fig. 1b) reveals that the nanowire surface was uniformly covered by clumps (a mat) of NiCo2S4 nanosheets (as confirmed by XRD and HRTEM observations below), forming a core-shell hierarchical nanostructure. As the sulfurization was prolonged to 36 h, the size of NiCo2S4 nanosheets increased. However, not all NiCo2S4 nanowires were covered by nanosheets. The uniform and large-scale NiCo2S4 CSNAs on Ni@G foam were obtained after sulfurization for 48 h, as shown in Fig. 1d. Enlarged SEM image inset Fig. 1d reveals that ultrathin NiCo2S4 nanosheets have a length of ~200 nm and a thickness of ~8 nm.

Figure 1
figure 1

SEM images of the nanowire arrays obtained for different sulfurization time:

(a) 12 h, (b) 24 h, (c) 36 h and (d) 48 h. Insets in (b,d) show the magnified images of hierarchical NiCo2S4 CSNAs after sulfurization for 24 and 48 h, respectively.

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Figure 2a shows XRD pattern of the as-synthesized hierarchical NiCo2S4 CSNAs scratched from Ni@G foam after sulfurization for 48 h. The diffraction peaks at 26.8°, 31.6°, 38.3°, 50.5° and 55.3° were indexed to the 220, 311, 400, 511 and 440 planes of the cubic NiCo2S4 with reference to the standard diffraction pattern of NiCo2S4 (Joint Committee on Powder Diffraction Standards (JCPDS) No. 20–0782). No other diffraction peaks were observed, verifying the formation of phase-pure NiCo2S4. The morphology and structure of hierarchical NiCo2S4 CSNAs after sulfurization for 48 h were further investigated by using TEM. Consistent with the SEM observations above, the low-magnification TEM images (Fig. 2b and Figure S3) confirm the formation of uniform core-shell hierarchical structure with the NiCo2S4 hollowed nanowire as core and NiCo2S4 nanosheets (height up to ~100–150 nm) as shell. Interestingly, it is noted that all of the NiCo2S4 core nanowires are mesoporous structure which is resulted from the replacement of O2− by S2− through sulfurization process30. The mesopores with a size ranging from 2 to 8 nm are uniformly distributed in the nanowires and nanosheets (Fig 2b,c), implying that the sulfurization processes homogeneously in the bulk of nanowires. HRTEM image in Fig. 2d further verified the crystal characteristics of NiCo2S4 nanostructures. As denoted in this figure, the interplane distances were measured to be 0.28 nm and 0.23 nm, which correspond to the d-spacing of (311) and (400) planes of cubic NiCo2S4, respectively. The TEM observations verified that the hierarchical nanostructure is composed of the same electrochemical materials in core and shell, wherein both the nanowire core and the nanosheets shell could contribute to electrochemical reactions for energy storage. Moreover, the hierarchical NiCo2S4 core-shell nanowires are featured with open spaces between shell nanosheets, which allow access of electrolyte to both core and shell surfaces and leads to improved electrochemical performance of active materials.

Figure 2
figure 2

Characterization of the hierarchical NiCo2S4 core-shell nanowires.

(a) XRD pattern of the hierarchical NiCo2S4 core-shell nanowires scratched from Ni@G foam. (b) TEM image of the hierarchical NiCo2S4 core-shell nanowire, (c) Enlarged TEM view and (d) HRTEM image of the joint area between NiCo2S4 nanowire and nanosheet.

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The surface area and porosity of hierarchical NiCo2S4 CSNAs scratched from Ni@G foam were examined with adsorption-desorption experiment using Brunauer-Emmett-Teller (BET) method (Figure S4). Following the Barrett-Joyner-Halenda (BJH) method, NiCo2S4 core-shell nanowires exhibited a pore size distribution ranging from 4 to 8 nm, which is consistent with the TEM observation in Fig. 2c. The specific surface area of hierarchical NiCo2S4 core-shell nanowires was calculated to be 84.9 m2/g, which is significantly higher than those of the other NiCo2S4 nanostructures reported in literatures18,19,31,32. A high specific surface area of active materials enables the efficient contact with electrolyte and increases the numbers of electroactive for charge storage and delivery.

The performance of electrochemical electrodes is known to depend strongly on the specific surface area and a well the electrical conductivity of the active materials1,2. In this work, the electric conductivity of an individual hierarchical NiCo2S4 core-shell nanowire was measured in situ in TEM using a specially design holder (Nanofactory Instruments AB). The experimental setup is sketched in Figure S5a and the other details have been reported in our previous work33,34. The hierarchical NiCo2S4 core-shell nanowire bridged Au tip and Pt probe by precisely adjusting Pt probe using a piezo-driven manipulator, as shown in Figure S5b. For comparison, a NiCo2O4 nanowire without nanosheets shell was also measured using the same method (inset Figure S5b, see the Supplementary Information II for Experimental details). The corresponding I-V curves were shown in Figure S5c. Both of the voltage range from −1.0 to 1.0 V, the current value of hierarchical NiCo2S4 core-shell nanowire varies from ~ −97.2 to 84.4 μA, while the current of NiCo2O4 nanowire varies from ~ −0.39 to 0.35 μA. Thus, the electrical conductivity of the NiCo2S4 core-shell nanowire is over 300 times higher than that of NiCo2O4 nanowire and about 4–5 orders of magnitude higher than those of metal oxides and sulfides in our previous work35,36.

A layer of carbon shell was deposited onto the surface of hierarchical NiCo2S4 CSNAs by hydrothermal method. As shown in Fig. 3a, the hierarchical NiCo2S4 CSNAs retained their morphology well after reaction for 3 h (see the Supplementary Information I for Experimental details). Enlarged SEM image in Fig. 3b reveals that the thickness of NiCo2S4 nanosheets is increased to 10–12 nm after carbon coating. Agreeing with the SEM observations, the low-magnification TEM image in Fig. 3c also demonstrates that the NiCo2S4 nanowires still maintain the core-shell structure with the nanowire cores uniformly covered by NiCo2S4. As further verified by the HRTEM image in Fig. 3d, a thin carbon layer shell with a thickness of 2–3 nm was deposited over the surface of hierarchical NiCo2S4 CSNAs. The thickness of carbon layer could be controlled by reaction time and it increased to 4–8 nm after reaction for 8 h (Fig. 3e).

Figure 3
figure 3

Characterization of the hierarchical NiCo2S4@C CSNAs.

(a,b) SEM images of the hierarchical NiCo2S4@C CSNAs after carbon coating by hydrothermal reaction for 3h. (c) TEM image of the carbon-coated hierarchical NiCo2S4@C CSNAs after hydrothermal deposition for 3h. HRTEM images of hierarchical NiCo2S4@C CSNAs samples with carbon layers deposited by hydrothermal reaction for: (d) 3 h and (e) 8 h.

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The electrochemical performance of hierarchical NiCo2S4@C CSNAs on Ni@G foam was studied in a standard three-electrode configuration using 1.0 M KOH electrolyte. The control experiments on reference samples of hierarchical NiCo2S4 CSNAs and NiCo2S4 nanowire arrays (NAs) on Ni@G foams were also performed (see the Supplementary Information III for Experimental details and Figure S6). Because the 4–8 nm thick carbon layer restrain the ions in electrolyte to penetrate through it and react with the NiCo2S4 CSNAs and leads to poor electrochemical performance (Figure S7), the following tests were conducted on the hierarchical NiCo2S4@C CSNAs with a thin carbon layer of 2–3 nm. Figure 4a presents the cyclic voltammetry (CV) curves of hierarchical NiCo2S4@C CSNAs electrode at different scan rates of 5, 10, 20, 30, 40 and 50 mV s−1 in a potential window of −0.2–0.6 V. The redox current increased with the increase of scan rate from 5 to 50 mV s−1 and the oxidation and reduction peaks shifted toward higher and lower potentials, respectively, resulting in an enlarged potential separation. The CV curves of hierarchical NiCo2S4 CSNAs and NiCo2S4 NAs electrodes displayed the same tendency at different scan rates (Figure S8a), which suggests the same redox mechanism as that of hierarchical NiCo2S4@C CSNAs. However, at the same scan rate, the NiCo2S4@C CSNAs electrode has obviously a much larger integrated area than those of NiCo2S4 CSNAs and NiCo2S4 NAs electrodes, which indicates that the hierarchical NiCo2S4@C CSNAs electrode has a higher capacity. We also studied the CV characteristics of pure Ni@G foam, as shown in Figure S9. It was revealed that the pure Ni@G foam exhibited a much low capacity, indicating that the Ni@G foam had negligible contribution to the overall capacity of hierarchical NiCo2S4@C CSNAs electrode.

Figure 4
figure 4

Electrochemical properties of NiCo2S4@C CSNAs, NiCo2S4 CSNAs and NiCo2S4 NAs electrodes in 1 M KOH aqueous solution at room temperature.

(a) The CV curves of NiCo2S4@C CSNAs electrode at different scan rates. (b) The CD curves of NiCo2S4@C CSNAs electrode at different current densities. (c) Specific capacities of NiCo2S4@C CSNAs (red curve), NiCo2S4 CSNAs (blue curve) and NiCo2S4 NAs (black curve) electrodes at different current densities. (d) Cycling properties of NiCo2S4@C CSNAs (red curve), NiCo2S4 CSNAs (blue curve) and NiCo2S4 NAs (black curve) electrodes at a scan rate of 50 mVs−1 in 5000 cycles.

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The galvanostatic charge-discharge (CD) tests of NiCo2S4@C CSNAs, NiCo2S4 CSNAs and NiCo2S4 NAs were performed in a potential window between 0 and 0.45 V at current densities ranging from 3 to 50 A g−1, as shown in Fig. 4b and Fig. S8. While close observation of the CV and CD curves of NiCo2S4@C CSNAs and NiCo2S4 CSNAs electrodes suggested both capacitive effect and ion-diffusion effect for the energy storage, further analysis on the dependence of the current (i) with the sweep rate (v) at a fixed potential in reduction processes verified that they are closer to the battery-type materials (Figure S10)37,38,39. So, in order to obtain real and accurate values of the energy storage, the capacities were calculated based on the battery equation (unit, mAh g−1). According to previously reported40, the specific capacity values of the electrode materials are calculated from the galvanostatic discharge curves at various current densities. The specific capacity of NiCo2S4@C CSNAs was calculated to be 253, 250, 228, 198, 182, 170 and 163 mAh g−1 at current densities of 3, 5, 10, 20, 30, 40 and 50 A g−1, respectively, as shown in Fig. 3c (red curve). The specific capacity of NiCo2S4 CSNAs and NiCo2S4 NAs electrodes at different current densities were also evaluated, as depicted by blue and black curves, respectively, in Fig. 4c. The specific capacity of hierarchical NiCo2S4@C CSNAs electrode is apparently higher than those of NiCo2S4 CSNAs and NiCo2S4 NAs electrodes for each current density. As the current densities increased from 3 to 50 A g−1, the rate capability of NiCo2S4@C CSNAs, NiCo2S4 CSNAs and NiCo2S4 NAs electrodes were reduced to 64.4%, 32.3% and 31.7%, respectively, of their original values, indicating that NiCo2S4@C CSNAs electrode has best rate capability. As a result, at the current density of 50 A g−1, the specific capacity of the NiCo2S4@C CSNAs ~2.3 times higher than that of the is NiCo2S4 CSNAs (163 mAh g−1 vs. 72 mAh g−1). The cycling stability of NiCo2S4@C CSNAs, NiCo2S4 CSNAs and NiCo2S4 NAs electrodes were evaluated by repeated charge/discharge measurements at a scan rate of 50 mVs−1, as shown in Fig. 4d. Interestingly, the overall loss of capacity of NiCo2S4@C CSNAs after 5000 cycles was less than 6.1%, i.e., the capacity retention of 93.9% over 5000 cycles, which is obviously superior to the NiCo2S4 CSNAs (73.3%) and NiCo2S4 NAs (74.6%) electrodes. The capacity retention of NiCo2S4 NAs is slightly higher than that of hierarchical NiCo2S4 CSNAs. On the one hand, high specific surface areas of active materials of NiCo2S4 CSNAs enable the efficient contact with electrolyte and increase the electroactive sites for redox reactions. On the other hand, compared with NiCo2S4 NAs, hierarchical NiCo2S4 CSNAs may result in structural change of nanosheets from nanowire cores more easily.

Discussion

The above results revealed that the hierarchical NiCo2S4 CSNAs electrodes have the following characteristics which have been demonstrated to be beneficial to improve the electrochemical perfromance27,28,29,41,42,43,44,45. First, both core and shell are active materials; and the 3D core-shell structure enables easy access of electrolyte. Therefore, both of them can effectively contribute to the capacity. Secondly, the hierarchical NiCo2S4 CSNAs are highly conductive, which can provide “superhighways” for charge in the core-shell structure. The direct growth of NiCo2S4 nanoshells on NiCo2S4 nanowires avoids the use of polymer binder/conductive additives and further guarantees the effective charge transport between them. Moreover, the NiCo2S4 shells and NiCo2S4 nanowires are mesoporous that increases the electroactive sites. Therefore, the hierarchical NiCo2S4 CSNAs/Ni@G electrode has a comparable or even superior performance to the previously reported electrodes based on nickel/cobalt sulfide nanomaterials40. Surface carbon coating could significantly further improve the overall electrochemical properties and made the hierarchical NiCo2S4@C CSNAs/Ni@G a very promising candidate for electrode applications.

In order to understand the degradation of electrochemical performance and beneficial role of surface carbon coating, we comparatively analyzed the variation of microstructure and chemical composition of the hierarchical NiCo2S4 CSNAs with and without carbon coating after 5000 charge/discharge cycles. The structures of NiCo2S4 CSNAs and NiCo2S4@C CSNAs electrodes after cycling at 50 mVs−1 were characterized by SEM and TEM. The morphology of the NiCo2S4 CSNAs mainly retained their array structure, but the increased diameter and roughness of NiCo2S4 nanowires after 5000 cycles, as shown in Fig. 5a and enlarged SEM image in Figure S11. However, TEM observation in Fig. 5b (more NiCo2S4 core-shell nanowires in Figure S12) reveals that the NiCo2S4 nanosheets were shortened to ~50–80 nm in height and shell nanosheets were detached from the core nanowires, forming a nanometer-scale gap between core and shell after 5000 cycles gaps, as denoted by the blue arrows. The breakdown of the hierarchical core-shell structure could possibly be caused by the repeated charge transfer through the core-shell interface during cycling processes which might induce uneven Joule heating and anisotropic volume expansion of nanowires and nanosheets of different geometric features.

Figure 5
figure 5

Characterization of the hierarchical NiCo2S4 CSNAs and NiCo2S4@C CSNAs after charge/discharge for 5000 cycles at a scan rate of 50 mV s−1.

(a) SEM image, (b) TEM image and (c) EDS pattern of the NiCo2S4 CSNAs electrode after charge/discharge for 5000 cycles at a scan rate of 50 mV s−1. (d) SEM image, (e) TEM image and (f) EDS pattern of the NiCo2S4@C CSNAs electrode after charge/discharge for 5000 cycles at a scan rate of 50 mV s−1.

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The redox reactions during repeated charge/discharge processes may lead to dissolution of NiCo2S4 into the electrolyte and an irretrievably chemical composition change of the NiCo2S4 . As shown by the EDS spectra for NiCo2S4 CSNAs electrode before (i) and after (ii) 5000 cycles in Fig. 5c, the contents of Ni and S decreased and O content increased drastically after cycling, suggesting the a variation of the chemical composition of NiCo2S4 (Figure S13). Figure S14 shows representative CV curves of NiCo2S4 CSNAs electrode in the voltage window of −0.2 to 0.6 V at a scan rate of 50 mV s−1 for the 1st, 1000th, 2000th, 3000th, 4000th and 5000th cycles. The locations of the pair of current peaks for faradic oxidation/reduction reactions shifted obviously from the 1st to 5000th cycle, which further verifies a gradual change in the chemical composition of NiCo2S4. In the aqueous solution of KOH, OH− ions and can serve as sources for the ion-exchange reaction to convert NiCo2S4 to (Ni, Co) hydroxide.

The redox reactions occurred in both surface and inside of NiCo2S4 nanosheets and nanowires, which may also result in the structural pulverization and detachment of nanosheet shell from nanowire core. The conversion of chemical composition from NiCo2S4 to oxide and deterioration of the core-shell structure caused the increase of the resistance of hierarchical NiCo2S4 CSNAs electrode after 5000 cycles as compared with that before cycling (as evidenced by EIS measurements in Figure S15). In addition, the specific surface area of hierarchical NiCo2S4 core-shell nanowires was also reduced to 38.9 m2/g after 5000 cycles (Figure S16), which is distinctly lower than that before charge/discharge processes (84.9 m2/g). As a result of the gradual conversion of NiCo2S4 to oxide with increased resistivity, the breakdown of the core-shell structure and the reduced surface area of the NiCo2S4 CSNAs electrode, the electrochemical performance of the NiCo2S4 CSNAs electrode, including specific capacity, rate capability and cycling stability, deteriorated after charge/discharge cycles.

As the NiCo2S4 CSNA electrodes were coated with a surface carbon layer, the NiCo2S4@C CSNAs still showed their hierarchical morphology after 5000 charge/discharge cycles (Fig. 5d). Interestingly, the TEM observation in Fig. 5e further revealed that the size of shell NiCo2S4 nanosheets preserved and the NiCo2S4 core-shell nanowires maintained their integrity without gaps formed at the core-shell interface. In a sharp contrast to the NiCo2S4 CSNA electrodes, the EDS spectra for the NiCo2S4@C CSNAs before (i) and after (ii) 5000 cycles in Fig. 5e indicated that the electrode had its chemical composition almost unchanged with only a slight increase of oxygen content after long-term cycling (Figure S17). Correspondingly, the two strong peaks for the faradic oxidation/reduction reactions the CV curves showed only slight shift from 1st to 5000th CV curves (as denoted in Figure S18), which also verifies an unchanged composition of NiCo2S4@C CSNAs. Based on these observations, the surface carbon layer was demonstrated to play important roles in slowing down the degradation of the NiCo2S4@C CSNA electrode. First, it could serve as a physical buffer layer to suppress the structural alternation and counteract the pulverization of hierarchical NiCo2S4 CSNAs. Second, it could function as a chemical blocking layer to retard the chemical composition conversion of the NiCo2S4 CSNAs during cycling. Finally, it could also provide extra path for direct charge transport to current collector in addition to the conductive NiCo2S4 core nanowires (Figure S19), which led to a lower resistivity of the hierarchical NiCo2S4@C CSNAs electrode than that of the NiCo2S4 CSNAs electrode (Figure S20). Compared with the NiCo2S4 CSNAs electrode (Figure S19a), the surface carbon layer in the NiCo2S4@C CSNAs electrode could also reduce repeated charge transfer through the core-shell interface, which could decrease the local Joule heat produced there and the resultant anisotropic volume expansions (-induced detachment of shell nanosheets from core nanowires) (Figure S19b). As a result, NiCo2S4@C CSNAs electrodes could have a much improved overall electrochemical performance including an increase of specific capacity by (253 mAh g−1 vs. 224 mAh g−1 at 3 A g−1 and 163 mAh g−1 vs. 72 mAh g−1 at 50 A g−1), the rate capability (64.4% vs. 32.3%) and cycling stability (retention of 93.9% vs. 73.3%).

We have successfully synthesized the hierarchical NiCo2S4@C CSNAs directly on Ni@G foams using hydrothermal reactions followed by a sulfurization process. The hierarchical NiCo2S4@C CSNAs electrode exhibits exceptionally high specific capacity (253 mAh g−1 at 3 A g−1), high rate capability (~64.4% retention from at 3 to 50 A g−1) and excellent cycling stability (6.1% capacity loss after 5000 cycles at 50 mVs−1). By comparatively studying the degradation of hierarchical NiCo2S4 CSNAs electrode with and without carbon coatings, we revealed that the morphology pulverization, structural separation at core/shell interface and irretrievably chemical composition change of NiCo2S4 CSNAs electrode during charge/discharge cycles are major factors that resulted in reduction of the specific capacity, deterioration of the rate capability and long-term cycling stability of the NiCo2S4 CSNAs electrodes. The surface carbon coating was demonstrated to be able to improve drastically the electrochemical performance of the NiCo2S4 CSNAs electrodes, which could serve as a physical buffering layer to suppress the structural breakdown, diminish the chemical composition conversion of the NiCo2S4 CSNAs and provide extra path for charge transition in addition to the NiCo2S4 core nanowires. The understanding of the degradation mechanism of the core-shell nanostructured electrodes and as well the beneficial roles of surface carbon coating will be helpful for the design and fabrication of new electrodes for high-performance electrochemical devices.

Methods

Synthesis

All chemicals were purchased from Sigma-Aldrich were used as received without further purification. The hierarchical NiCo2S4 CSNAs, hierarchical NiCo2S4@C CSNAs and NiCo2O4 NAs were synthesized on Ni@G foam using hydrothermal reactions followed by a simple sulfurization treatment. The detailed conditions, e.g, source materials, processing temperature and time, are provided in Supplementary Information I, II and III. The loading weight of hierarchical NiCo2S4 CSNAs and hierarchical NiCo2S4@C CSNAs was about 3.4–3.6 mg cm−2.

Characterization

The as-synthesized products were characterized with a D/max-2550 PC X-ray diffractometer (XRD; Rigaku, Cu-Ka radiation), a scanning electron microscope (SEM; S-4800), a transmission electron microscope (TEM; JEM-2100F) equipped with an energy dispersive X-ray spectrometer (EDX) and an X-ray photoelectron spectrometer (ESCALab MKII) with an excitation source of Mg-K radiation. The surface area and pore size distribution of the products were determined by Brunauer-Emmett-Teller (BET) nitrogen adsorption-desorption and Barrett-Joyner-Halenda (BJH) methods (Micromeritics, ASAP2020). The electrical properties of samples were tested in situ by using a TEM-scanning tunneling microscope (TEM-STM) holder (commercialized by Nanofactory Instruments AB, GÖteborg, Sweden), which was arranged within a 200 kV high resolution TEM (JEM-2100F) with beam-blank irradiation of a low illumination.

Electrochemical measurements

Electrochemical measurements were performed on an Autolab Electrochemical Workstation (PGSTAT302N) using a three electrode electrochemical cell and 1 M KOH as the electrolyte. The Ni@G foam supported electroactive materials (1 cm × 1 cm) were directly used as the working electrode. A saturated calomel electrode (SCE) was used as the reference electrode and a platinum (Pt) sheet was used as the counter electrode. All potentials were referred to the reference electrode. The specific capacity and current density were calculated based on the mass of these electroactive materials.

Additional Information

How to cite this article: Zou, R. et al. Electrochemical Energy Storage Application and Degradation Analysis of Carbon-Coated Hierarchical NiCo2S4 Core-Shell Nanowire Arrays Grown Directly on Graphene/Nickel Foam. Sci. Rep. 6, 20264; doi: 10.1038/srep20264 (2016).