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Article

NiS1−xSex Nanoparticles Anchored on Nitrogen-Doped Reduced Graphene Oxide as Highly Stable Anode for Sodium-Ion Battery

by
Shunjiang Zhang
,
Ruirui Wang
,
Ronggen Cao
*,
Fang Fang
and
Renbing Wu
Department of Materials Science, Fudan University, Shanghai 200433, China
*
Author to whom correspondence should be addressed.
Processes 2022, 10(3), 566; https://doi.org/10.3390/pr10030566
Submission received: 10 February 2022 / Revised: 7 March 2022 / Accepted: 9 March 2022 / Published: 14 March 2022
(This article belongs to the Special Issue State of the Art of Energy Storage and Conversion Materials)
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Abstract

:
Nickel sulfides are regarded as one of the promising anode materials for sodium-ion batteries (SIBs), but the sluggish electrodes kinetics and rapid capacity decay, caused by their intrinsic low electrical conductivity and high bulk expansion, greatly limit their practical application. To overcome these obstacles, nano-sized, selenium-doped, nickel sulfide particles, anchored on nitrogen-doped reduced graphene oxide composites (NiS1−xSex@N–rGO), are rationally synthesized. The broad Na+ diffusion channels, resulting from Se doping, as well as the short Na+ transferring path, attributed from nano-size scale of NiS1−xSex particles, endow NiS1−xSex@N–rGO composites with ultrafast storage kinetics. Moreover, strong coupled effect between the NiS1−xSex and N–rGO is beneficial to the uniform dispersion of NiS1−xSex nanoparticles, improving electrical conductivity and suppressing the volume variation in charge/discharge process. Furthermore, the cut-off discharge voltage is modulated to realize the smaller volume change during cycle process. As a result, the fabricated anode of SIBs based on NiS1−xSex@N–rGO composites exhibits a high specific capacity of 300 mAh g−1, at the current density of 1 A g−1, after 1000 cycles with almost no capacity degradation.

1. Introduction

Lithium-ion batteries (LIBs) have been extensively applied in all aspects of our lives, but the limited lithium resources cannot satisfy the ever-growing demand for future electrical storage system (EES) devices [1,2,3,4,5,6]. Sodium-ion batteries (SIBs) are deemed to be a highly promising alternative, due to the abundant resources, low-cost and, especially, similar working mechanism to LIBs [7,8,9]. However, graphite, as the conventional anode material of LIBs, is eliminated for SIBs, due to the larger atomic radius of sodium element [10,11,12]. Therefore, it is imperative to develop appropriate anode materials for SIBs. In the past years, a variety of anode materials, including hexagonal boron nitride (h–BN) [13], carbonaceous materials [14,15], alloy-based materials [16,17], transition metal oxides [18,19,20], and transition metal chalcogenides [21,22,23], have been explored as anode materials for SIBs. Among them, transition metal chalcogenides, especially nickel sulfides, have received much attention, due to their high specific capacity, rich resources, low-cost, and being environmentally benign [24,25,26,27]. However, the nickel sulfides suffer from a poor electrical conductivity and large volume expansion during charge/discharge process, leading to unsatisfactory specific capacity and fast capacity fading [9,28,29].
In order to address the above-mentioned issues, several effective strategies have been developed. The first one is optimizing nanostructure by reducing the size of materials to nanoscale, leading to a short ion-diffusion path and minimizing the effect of volume expansion [17,30]. The second one is introducing carbon matrix by compositing nickel-based sulfides with conductive carbon materials, such as graphene, carbon nanotube, and porous carbon, which demonstrated great promise in enhancing the electrical conductivity and inhibiting the volume change [31,32]. The third one is tailoring chemical composition by doping with homologous nonmetallic elements, which not only boosts electrochemical activity but also significantly improves the physicochemical properties of various alkali ion transport [33,34,35]. For example, Yang et al. synthesized solid-solution FeS2−xSex microspheres as an anode material for SIBs. Benefiting from the increased layer spacing and improved electronic conductivity, the electrodes exhibited 275 mAh g−1 after 1000 cycles at 1 A g−1 [36]. Cao et al. reported Se-doped, nickel–cobalt sulfides for high-performance supercapacitor, demonstrating fast ion diffusion and low resistance characteristics after Se doping [37]. Furthermore, according to present studies, electrode materials suffer from irreversible loss of capacity and greater volume expansion under the fully discharged condition, so selecting a suitable cut-off discharge voltage would be beneficial to realize better cycling stability [12]. Despite the achievements that have been made, limited improvement of the sodium storage properties of nickel sulfides were achieved by each proposed strategy along, and the integration of all above-mentioned strategies remains a big challenge.
Herein, nano-sized, selenium-doped, nickel sulfide particles anchored on nitrogen-doped reduced graphene oxide (NiS1−xSex@N–rGO) were successfully synthesized by hydrothermal reaction and subsequent sulfuration/selenization reaction. Benefiting from the nano-sized scale, broaden ion diffusion channels and strong coupling effect between NiS1−xSex nanoparticles and N–rGO, the NiS1−xSex@N–rGO composites possess enhanced electrochemical reaction kinetics and mitigated volume variation during cycling process. As expected, the obtained NiS1−xSex@N–rGO composites, used as the anode material for SIBs, maintained a stable specific capacity of 300 mAh g−1, after 1000 cycles 1 A g−1, through regulating the cut-off discharge voltage.

2. Materials and Methods

2.1. Preparation of Spongy Ni(OH)2@GO Precursor

Firstly, nickel nitrate hexahydrate (1 mmol) and 2–Methylimidazole (2–MeIm, 4 mmol) were dissolved in 5 mL CH3OH, respectively, denoted as solutions A and B. Secondly, solutions A and B were successively added into 17 mL GO aqueous suspension (4 mg mL−1), which was stirred for 10 min at room temperature to form suspension C. Then, suspension C was transferred into Teflon-lined autoclave and maintained at 180 °C for six hours. After cooled to room temperature, the black samples of Ni(OH)2@GO was centrifuged and washed twice with CH3OH and H2O. Lastly, the obtained Ni(OH)2@GO was blended with appropriate amounts of H2O and freeze-dried at −50 °C for two days to obtain the spongy Ni(OH)2@GO.

2.2. Preparation of NiS1−xSex@N–rGO Composites

The spongy Ni(OH)2@GO precursor and sulfur/selenium powder were placed at the head and last sides of a porcelain boat, then heated to 600 °C (2 °C min−1), and they maintained this temperature for two hours in a flowing nitrogen atmosphere. Gaseous sulfur and selenium were driven by flowing nitrogen gas to react with the Ni(OH)2@GO precursor to form the NiS1−xSex@N–rGO composite. The preparation of NiS@N–rGO comparison samples was similar to NiS1−xSex@N–rGO, except the absence of selenium powder.

2.3. Materials Characterizations

To observe the microstructure of the obtained samples, the field emission scanning electron microscope (FESEM, ZEIS, super–55) and transmission electron microscope (TEM, JEOL–2100) were employed. The phase composition was tested by X-ray diffractometer (XRD, D8 ADVANCE, Cu Kα–ray). The Raman spectra were measured on a Witec Alpha 300. The nitrogen adsorption–desorption isotherms measurement was performed on a JW–BK 100C instrument. The elemental states of samples were investigated using an X-ray energy spectrometer (Thermo Scientific, USA, ESCALAB 250XI). The weight loss curves of NiS1−xSex@N–rGO and NiS@N–rGO composites were obtained by thermogravimetric analysis (MET–TLER TOLEDO TGA2).

2.4. Electrochemical Measurements

In order to fabricate working electrodes, the active material (NiS1−xSex@N–rGO, 70 wt%), conductive carbon black (super–p, 20 wt%), and polyvinylidene fluoride (PVDF, 10 wt%) were dispersed in N-methyl pyrrolidone (NMP) solvent to make a slurry. The above prepared slurry was coated on the copper foil and then dried in vacuum at 70 °C for 12 h, which was subsequently cut into round films to be used as working electrodes. The half-cells were assembled in an argon-filled glove box (<0.5 ppm, H2O and O2). Na foil, Whatman glass fiber and 0.5 M NaCF3SO3 were utilized as counter electrode, separator, and electrolyte, respectively. The sodium storage performance at ambient temperature and effect of different voltage range (0.01–3.0 V and 0.3–3 V) for the assembled cells were obtained using the Land CT2001A battery testing system. AutoLab PGSTAT302N was employed to obtain the CV and EIS curves.

3. Results

The overall synthetic route for the synthesis of NiS1−xSex@N–rGO composites is illustrated in Figure 1. First, the precursor of Ni(OH)2, anchored on the surface of graphene oxide (Ni(OH)2@GO), was fabricated by a simple hydrothermal reaction. It is noticed that 2-Methylimidazole (2-MeIm) was served as the nitrogen source and can facilitate the generation of sheet-like Ni(OH)2 [38]. After a sulfuration/selenization reaction at high temperature (N2 atmosphere), the Ni(OH)2 was directly transformed into NiS1−xSex nanoparticles, and the GO was transformed into N–rGO simultaneously.
The morphology and microstructure of the obtained samples were observed by FESEM and TEM. The FESEM images of Ni(OH)2@GO precursors can be seen from Figure S1a,b. It is found that the sheet-like Ni(OH)2 with smooth surface was compactly coated on the surface of GO, demonstrating a strong interaction force between them. After a sulfuration/selenization reaction, Ni(OH)2@GO precursor was transformed into NiS1−xSex nanoparticles, uniformly anchored on N–rGO (Figure 2a,b). The NiS@N–rGO presented a similar structure with that of NiS1−xSex@N–rGO composite (Figure S1c,d). The TEM images further demonstrated the homogeneous distribution of NiS1−xSex nanoparticles with diameters of 50–100 nm on N–rGO nanosheet (Figure 2c). In contrast, NiS1−xSex particles, converted from Ni(OH)2, were gathered seriously (Figure S2), indicating that the addition of GO can serve to uniformly disperse the NiS1−xSex nanoparticles. Additionally, the lattice fringes with 0.281 nm can be clearly observed in Figure 2d, which corresponds to the (101) crystal plane of NiS. The fast Fourier transform (FFT) pattern (inset of Figure 2d) also confirmed the (101) crystal plane of NiS. However, the lattice spacing was slightly larger than that of standard NiS, indicating that Se elements with a larger radius were successfully doped into the lattice of NiS in NiS1−xSex@N–rGO composites. Moreover, elemental mapping images revealed that Ni, Se, S, N, and C elements were well-distributed in the NiS1−xSex@N–rGO composites (Figure 2e–j), further confirming the well-doping of Se into NiS and successful synthesis of NiS1−xSex@N–rGO composites.
In order to analyze the phase composition of the obtained samples, XRD characterization was implemented. Figure S3 was the diffraction peaks of the Ni(OH)2@GO precursor, which was consistent with the crystallographic data of Ni(OH)2 (JCPDS Card No. 14-0117). Five main peaks at 19.3°, 33.1°, 38.5°, 39.1°, and 52.1° can be attributed to the (001), (100), (101), (002), and (102) crystal planes of Ni(OH)2. The NiS@N–rGO and NiS1−xSex@N–rGO composites show similar crystal structure, corresponding to hexagonal NiS (JCPDS Card No. 02–1280). However, the diffraction peaks of the NiS1−xSex@N–rGO composites shifted to a smaller angle, compared to the peaks of NiS, suggesting that the Se with a larger ionic radius (1.98 Å) was doped into NiS and enlarged the lattice spacing, without disturbing the crystal structure in the NiS1−xSex@N–rGO composites. To further demonstrate the successful doping of selenium, thermogravimetric analysis (TGA) characterization was conducted. As shown in Figure 3b, the TGA curves of the NiS@N–rGO and NiS1−xSex@N–rGO composites exhibited similar weight loss trend, with the temperature increasing in O2 atmosphere, except in the temperature range of 550–670 °C. In this temperature range, the NiS@N–rGO composites underwent a conversion reaction from nickel sulfide to nickel sulfate, followed by a partial decomposition reaction of nickel sulfate to nickel oxide, but the NiS1−xSex@N–rGO composites were also accompanied by the breakdown of the Ni–Se bond [12,35,39].
The Raman spectra of NiS1−xSex@N–rGO and NiS@N–rGO are shown in Figure 3c. Two distinct peaks of graphite can be observed at ~1350 (D-band) and ~1580 cm−1 (G-band), which correspond to the disordered carbon and ordered graphitic carbon, respectively [40,41]. The peak intensity ratio (ID/IG) of NiS1−xSex@N–rGO (1.16) is slightly higher than that of NiS@N–rGO (1.12), implying the abundance of defects and vacancies in NiS1−xSex@N–rGO, which is favorable to improving the sodium storage kinetics [33,42]. The N2 gas adsorption–desorption methodology was employed to investigate the porosity structure of NiS1−xSex@N–rGO composites, and the result was presented in Figure 3d and Figure S4. The Brunauer–Emmett–Teller (BET) surface area of the NiS1−xSex@N–rGO composites is as high as 431.7 m2 g−1 (which is larger than 189.6 m2 g−1 of NiS@N–rGO). Additionally, the pore size distribution of both is concentrated at ~2 nm (inset of Figure 3d and Figure S4b). Such a high BET surface area of NiS1−xSex@N–rGO can be attributed to the three-dimensional structure of interconnected graphene and uniformly distribution of optimal pores. Importantly, this favorable structure can provide enough free space to accommodate the volume expansion of the NiS1−xSex nanoparticles during the cycle process and may greatly facilitate the penetration of the electrolyte.
To verify the chemical state and elemental composition of obtained samples, X-ray photoelectron spectroscopy (XPS) was performed. The surface chemical composition of the NiS1−xSex@N–rGO composites can be accessed from Figure 4. It is evident that Ni, Se, S, C, and N elements all exist in NiS1−xSex@N–rGO composites (Figure 4a). Notably, the peaks positions of C 1s (Figure 4b) and N 1s (Figure 4c) in NiS@N–rGO and NiS1−xSex@N–rGO composites are well in accordance with each other, suggesting the consistent chemical states of N–rGO in them. As seen in Figure 4b, three peaks located at 284.6, 285.6, and 286.3 eV were ascribed to the C–C, C–O, and C–N bonds, respectively [24,41]. As for the N 1s XPS spectrum in Figure 4c, three peaks at 399.0 eV, 400.8 eV, and 402.6 eV were assigned to pyridinic N, pyrrolic N, and graphitic N, respectively [43]. Importantly, due to the existing of the conjugation between the lone pair of electrons of the N atom and large π-bonds of the reduced graphene oxide lattice, the nitrogen doped in the reduced graphene oxide can enhance the electronic conductivity and provide more reactive sites [23,27,44,45,46,47].
The high-resolution Ni 2p XPS spectra of NiS1−xSex@N–rGO and NiS@N–rGO composites can be observed in Figure 4d. For NiS1−xSex@N–rGO composite, the Ni 2p XPS spectrum showed five deconvoluted peaks. Two representative peaks at 852.9 and 855.0 eV were belong to Ni 2p3/2, while the peak at 872.8 eV were related to Ni 2p1/2 [48,49]. In addition to above three peaks, two accompanying satellite peaks at 860.5 and 879.8 eV were also observed. It was noticed that all the binding energy of Ni 2p3/2 and Ni 2p1/2 of NiS1−xSex@N–rGO composites were slightly lower than those of NiS@N–rGO composites (Ni 2p3/2: 853.3 and 855.5 eV, Ni 2p1/2: 870.2 and 873.5 eV), implying that the homogeneous doping of Se with lower electronegativity reduces the binding energy of nickel ions. For the high-resolution S 2p spectrum of NiS1−xSex@N–rGO (Figure 4e), the two major peaks located at 160.9 and 163.1 eV were attributed to S 2p3/2 and S 2p1/2, respectively, which are shifted to smaller binding energy, compared to those of peaks NiS@N–rGO (161.6 and 163.7 eV), suggesting the electronic structure of S element can be influenced by the Se element, with lower electronegativity. Additionally, two peaks at 159.3 and 165.8 eV in S 2p spectrum of NiS1−xSex@N–rGO were ascribed to the accompanying satellite peak of S 2p and S–O band. The peaks change of Ni 2p and S 2p indicates that the uniformly doping of Se with lower electronegativity into the NiS can decrease the binding energy of NiS, which is highly beneficial to the conversion reaction [50]. The high-resolution Se 3d spectrum of NiS1−xSex@N–rGO in Figure 4f can be divided into two well-fitted Se 3d5/2 and Se 3d3/2 peaks (located at 54.1 and 54.9 eV). The peak at 58.7 eV corresponds to the Se–O bond, reflecting the oxidation of the surface Se [49,50,51].
Inspired by the unique structural superiority, NiS1−xSex@N–rGO composites was assessed as anode materials for SIBs, and the effect of cut-off discharge voltage for the electrochemical performance was investigated. The cyclic voltammetry (CV) curves were first collected with a scan rate of 0.1 mv s−1, in two voltage ranges of 0.01–3 V and 0.3–3 V, respectively. In the first cathodic scan, in a voltage range of 0.01–3 V (Figure S5), an obvious peak can be seen located at 1.02 V, corresponding to the sodium ion insertion of NiS1−xSex@N–rGO (NiS1−xSex + γNa+ + γe− ↔ NaγNiS1−xSex, NaγNiS1−xSex + (2 − γ)Na+ + (2 − γ)e− ↔ Ni + (1 − x)Na2S + xNa2Se) and irreversible reaction associated with solid electrolyte interphase (SEI) formation [52,53,54]. In the first anodic scan, two broad peaks at 1.36 V, 1.79 V, and 2.25 V were associated with the oxidation reaction of Ni and the desodiation process [23,24,55,56]. The NiS1−xSex@N–rGO composites, in the range of 0.3–3 V (Figure 5a), showed similar curves, compared to that at voltage range of 0.01–3 V, but the CV curves shape in subsequent cycles presented a stronger tendency to overlapping, suggesting a more stable reaction in the NiS1−xSex@N–rGO electrode when the cut-off discharge voltage is 0.3 V [12]. In addition, Figure 5b provided the Coulombic efficiency for the first twenty charge/discharge cycles of NiS1−xSex@N–rGO electrode at different cut-off discharge voltages at 0.2 A g−1. It can be found that the Coulombic efficiency, under a cut-off discharge voltage of 0.3 V, is evidently higher in the first four cycles, while consistent in the following sixteen cycles, compared with that under the cut-off discharge voltage of 0.01 V, stating that a higher cut-off discharge voltage can avoid the occurrence of side reactions and, thus, increase the Coulombic efficiency.
Figure 5c shows the cycling performance of the NiS1−xSex@N–rGO electrode at 0.2 A g−1. It can be seen that the electrode maintained a high specific capacity of 305 mAh g−1 after 100 cycles when the cut-off discharge voltage is 0.3 V. However, as the cut-off discharge voltage is reduced to 0.01 V, the initial capacity is high (652 mAh g−1), but the capacity rapidly decayed to 140 mAh g−1 after 80 cycles. The rate performance of the NiS1−xSex@N–rGO electrode at different voltage range was also evaluated. As shown in Figure 5d, when employing a voltage range of 0.01–3 V, the average specific capacities were 507, 442, 391, 329, and 246 mAh g−1 at the current density of 0.2, 0.5, 1, 2, and 5 A g−1, respectively. When the current density returned to 0.2 A g−1, a normal specific capacity of 398 mAh g−1 was recovered, which is only 78.5% of the initial capacity. When employing the voltage range of 0.3–3 V, the ratio is 89.1%, indicating that the electrode material has superior reversibility in the voltage range of 0.3–3 V.
Figure 5e displays the cycling stability of NiS1−xSex@N–rGO and NiS@N–rGO at 1 A g−1. The NiS1−xSex@N–rGO electrode could deliver a stable specific capacity of 300 mAh g−1 after 1000 cycles, with almost no capacity decay, when the electrodes were tested at the voltage range of 0.3–3 V. This cycling performance far surpasses that of NiS@N–rGO (200 mAh g−1 after 1000 cycles) and is also better than the previously reported transition metal-based sulfide and selenide anodes (Table S1). Meanwhile, the cycling performance of NiS1−xSex@N–rGO at the voltage range of 0.01–3 V was also evaluated, which showed evident capacity fading and almost no capacity loss after 1000 cycles. The excellent cycling performance of NiS1−xSex@N–rGO is ascribed to the structural advantage and optimal cut-off discharge voltage. First, the nanoscale of NiS1−xSex particles shorten the migration distance of Na+, and Se-doping provides broad channels for Na+ diffusion, which endows NiS1−xSex@N–rGO with ultrafast storage kinetics. Second, N–rGO not only improves the electrical conductivity of the NiS1−xSex particle, but also suppresses their volume expansion during the charging and discharging process. Finally, the cut-off discharge voltage of the battery was optimized to achieve smaller volume expansion of NiS1−xSex during cycling process. In addition, to better understand the effect of Se doping for reaction kinetics of NiS, electrochemical impedance spectroscopy (EIS) tests were performed. As can be seen in Figure S6, NiS1−xSex@N–rGO electrode has a smaller charge transfer resistance and Na+ diffusion resistance, compared with that of NiS@N–rGO, revealing that the NiS1−xSex@N–rGO electrodes possesses excellent electrical conductivity and feasible Na+ ion diffusion ability.

4. Conclusions

In summary, we have developed an advanced anode material of SIBs, consisting of selenium-doped NiS nanoparticles, homogeneously anchored on nitrogen-doped reduced graphene oxide (NiS1−xSex@N–rGO), through a facile hydrothermal and sulfuration/selenization process. In these delicate hybrid composites, the rGO can induce a synergistic coupling effect with nano-sized NiS1−xSex, improving the electrical conductivity and alleviating the volume change. More importantly, Se doping into the NiS crystal structure led to broadened Na+ channels and enhanced conversion reaction kinetics. Therefore, the NiS1−xSex@N–rGO electrodes exhibit a highly stable specific capacity of 300 mAh g−1, after 1000 cycles at 1 A g−1, with almost no capacity degradation, by controlling the cut-off voltage (0.3–3.0 V).

Supplementary Materials

The following supporting information can be downloaded at: https://www.mdpi.com/article/10.3390/pr10030566/s1. Table S1: Electrochemical performance of the NiS1−xSex@N–rGO composite electrode, compared with the previously reported metal sulfide and metal selenide electrodes. Figure S1: (a,b) FESEM images of the Ni(OH)2@GO precursor, and (c,d) FESEM images of NiS@N–rGO. Figure S2: FESEM images of (a,b) pure Ni(OH)2 and (c,d) pure NiS1−xSex. Figure S3: XRD pattern of Ni(OH)2@GO precursor. Figure S4: (a) N2 sorption isotherms. (b) Pore size distribution of NiS@N–rGO composites. Figure S5: CV curves of NiS1−xSex@N–rGO electrode at 0.01–3 V. Figure S6: Electrochemical impedance spectra of NiS1−xSex@N–rGO and NiS@N–rGO electrodes.

Author Contributions

Conceptualization, S.Z., R.W. (Ruirui Wang), and R.C.; methodology, R.C.; validation, R.W. (Ruirui Wang); investigation, F.F. and R.W. (Renbing Wu); resources, R.C.; data curation, S.Z.; writing—original draft preparation, S.Z.; writing—review and editing, R.W. (Ruirui Wang) and R.W. (Renbing Wu); supervision, R.C.; project administration, R.C.; funding acquisition, R.C. and R.W. (Renbing Wu). All authors have read and agreed to the published version of the manuscript.

Funding

This work was financially supported by the National Natural Science Foundation of China (Grant No. 52071087).

Data Availability Statement

Not applicable.

Conflicts of Interest

The authors declare no conflict of interest.

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Figure 1. Schematic process of the formation of NiS1−xSex@N–rGO composites.
Figure 1. Schematic process of the formation of NiS1−xSex@N–rGO composites.
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Figure 2. (a,b) FESEM, (c) TEM, (d) HRTEM and FFT pattern, and (e–j) elements mapping images of NiS1−xSex@N–rGO composites.
Figure 2. (a,b) FESEM, (c) TEM, (d) HRTEM and FFT pattern, and (e–j) elements mapping images of NiS1−xSex@N–rGO composites.
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Figure 3. (a) XRD patterns, (b) TGA curves, (c) Raman spectra of NiS@N–rGO and NiS1−xSex@N–rGO composites. (d) N2 sorption isotherms and pore size distribution of NiS1−xSex@N–rGO composites.
Figure 3. (a) XRD patterns, (b) TGA curves, (c) Raman spectra of NiS@N–rGO and NiS1−xSex@N–rGO composites. (d) N2 sorption isotherms and pore size distribution of NiS1−xSex@N–rGO composites.
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Figure 4. (a) XPS survey spectrum of NiS1−xSex@N–rGO. (b–e) High-resolution C 1s, N 1s, Ni 2p, and S 2p contrast of NiS@N–rGO and NiS1−xSex@N–rGO composites. (f) Se 3d XPS spectrum of NiS1−xSex@N–rGO composites.
Figure 4. (a) XPS survey spectrum of NiS1−xSex@N–rGO. (b–e) High-resolution C 1s, N 1s, Ni 2p, and S 2p contrast of NiS@N–rGO and NiS1−xSex@N–rGO composites. (f) Se 3d XPS spectrum of NiS1−xSex@N–rGO composites.
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Figure 5. (a) CV curves at 0.3–3 V of NiS1−xSex@N–rGO. (b) Coulombic efficiency at 0.2 A g−1. (c,d) the cycling performance at 0.2 A g−1 and rate performance of the NiS1−xSex@N–rGO electrode at different cut-off voltages. (e) The cycling performance of NiS1−xSex@N–rGO and NiS@N–rGO electrode at 1 A g−1.
Figure 5. (a) CV curves at 0.3–3 V of NiS1−xSex@N–rGO. (b) Coulombic efficiency at 0.2 A g−1. (c,d) the cycling performance at 0.2 A g−1 and rate performance of the NiS1−xSex@N–rGO electrode at different cut-off voltages. (e) The cycling performance of NiS1−xSex@N–rGO and NiS@N–rGO electrode at 1 A g−1.
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Zhang, S.; Wang, R.; Cao, R.; Fang, F.; Wu, R. NiS1−xSex Nanoparticles Anchored on Nitrogen-Doped Reduced Graphene Oxide as Highly Stable Anode for Sodium-Ion Battery. Processes 2022, 10, 566. https://doi.org/10.3390/pr10030566

AMA Style

Zhang S, Wang R, Cao R, Fang F, Wu R. NiS1−xSex Nanoparticles Anchored on Nitrogen-Doped Reduced Graphene Oxide as Highly Stable Anode for Sodium-Ion Battery. Processes. 2022; 10(3):566. https://doi.org/10.3390/pr10030566

Chicago/Turabian Style

Zhang, Shunjiang, Ruirui Wang, Ronggen Cao, Fang Fang, and Renbing Wu. 2022. "NiS1−xSex Nanoparticles Anchored on Nitrogen-Doped Reduced Graphene Oxide as Highly Stable Anode for Sodium-Ion Battery" Processes 10, no. 3: 566. https://doi.org/10.3390/pr10030566

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