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Scale-Up Strategy to Develop Highly-Effective Co-N-C@KB Composites as Sulfur Host for Lithium-Sulfur Battery

Xiao-Xiang LU Tian-Bao LI Fei-Yue TU Zhong-Liang LI Xu-Kun ZHU Can SUN Ya-Chao JIN Li SONG Ming-Dao ZHANG Hui CAO

Citation:  Xiao-Xiang LU, Tian-Bao LI, Fei-Yue TU, Zhong-Liang LI, Xu-Kun ZHU, Can SUN, Ya-Chao JIN, Li SONG, Ming-Dao ZHANG, Hui CAO. Scale-Up Strategy to Develop Highly-Effective Co-N-C@KB Composites as Sulfur Host for Lithium-Sulfur Battery[J]. Chinese Journal of Inorganic Chemistry, 2021, 37(6): 1125-1134. doi: 10.11862/CJIC.2021.105 shu

用于鋰硫電池高效硫載體的Co-N-C@KB復合材料的規?;苽洳呗?/h2>
    通訊作者: 宋力, songli@nuist.edu.cn
    張明道, matchlessjimmy@163.com
    曹暉, jinyachao@nuist.edu.cn
  • 基金項目:

    國家自然科學基金 21905139

    國家自然科學基金 51902166

摘要: 硫正極較差的性能嚴重阻礙了鋰硫電池的商業化進程,這些因素包括較低的導電能力以及在促進多硫化物轉化方面較差的催化活性。我們開發了一種基于配體調控合成和低溫熱解的規?;呗詠碇苽涓咝У恼龢O復合材料(Co-N-C@KB),這種材料由富含Co-N-C活性位點的科琴黑(KB)組成。原子級分散的Co-N-C活性位點被證明有利于多硫化物在正極的轉化,因而可以提高鋰硫電池的容量和循環壽命?;诖?,Co-N-C@KB作為正極可以使鋰硫電池獲得高達1 442 mAh·g-1的初始放電容量,并且該電池在長時間的穩定性測試中具有出色的容量保持能力。

English

  • In recent years, lithium-sulfur (Li-S) battery has been praised as one of the most promising next-generation energy-storage systems, due to its prominent theoretical specific capacity (1 675 mAh·g-1) and energy density (2 615 Wh·kg-1) [1-2]. The characteristics, including low cost, easily-acquired electrode materials and environmental friendliness give lithium-sulfur battery an obvious edge over other candidates in the fields of electronic devices, unmanned aerial vehicles and new energy vehicles[3-5]. Although the theoretical energy density of Li-S battery has surpassed that of the conventional lithium-ion battery, the challenges at the sulfur cathode and lithium anode still hinder the industrial application of Li-S battery[6-8]. Due to the low conduc-tivity of sulfur and its reduction products (Li2S/Li2S2), the utilization efficiency of active substances in Li-S batteries is low and it is difficult to reach the theoretical specific capacity[9-10]. Besides, the charging and discharging processes at the sulfur cathode include multistep redox reactions, and the appearance of soluble polysulfide will cause shuttle effect, leading to the low utilization rate of sulfur and shortening battery life[11].

    At present, fabricating sulfur-based cathodes with superior performance has become one of the main orientations to ameliorate the Li-S batteries. The most commonly used method is to embed sulfur into high specific-surface nanocarbon, including ordered meso-porous carbon, carbon nanotubes[12-15], graphene[16] and metal-organic-framework (MOF) derived carbon materials[17-18]. Although excellent conductivity of these carbon materials evidently enhances the battery performance, weak physical interaction between nonpolar carbon and the polar lithium polysulfide still cannot block the occurrence of shuttle effect. In the subsequent studies, it was proved that some transition metals (Co[19-21], Ni[22-23] and Mo[24-25]), especially atomically dispersed metal on the carbon matrix[26-29], can be em-ployed as the electrocatalysts for rapid conversion of polysulfide, which suppresses the shuttle effect and enhances the capacity of collecting polysulfide, therefore improving the cycling stability and capacity of Li-S batteries. Based on this, Ma et al.[30] synthesized a polysulfide mediator composed of nitrogen-doped carbon nanotube (N-CNT) forest planted on cobalt nanoflowers (N-CNTs/Co-NFs), used as an efficient sulfur host material for Li-S batteries. Li et al. [31] synthesized a three-dimensional porous nitrogen-doped carbon polyhedron (Co/CoP@NC) and proved that the doping of Co transition metal exhibits strong chemisorption capacity with sulfur species and electrocatalytic effect for polysulfide conversion. Chen et al.[32] developed a scalable process to prepare a composite with Co-nanoparticle-embedded and nitrogen-doped carbon nanotube/nano-polyhedra (Co-NCNT/NP) superstructures, which provides the idea for mass preparation of efficient sulfur host materials.

    Inspired by these works, the carbon composite material coupled with uniformly dispersed transition metal atoms can be prepared and used as the effective sulfur host material at a very low cost. In this work, a ligand - mediated synthesis procedure was developed to capture the Co ions in the precursor, followed with a low-temperature-pyrolysis process, and this would result in uniformly dispersed Co-N-C sites on the carbon support. Via utilization of the cheap ligand of 2, 2'-bipyridine, a close relationship can be built between the ligands and metal cations, which would lead to the formation of Co-N-C species supported on the carbon after the process of 600 ℃ pyrolysis. This strategy can effectively alleviate the agglomeration of Co. As a result, the composite materials possess excellent electrical conductivity benefited from the carbon support and strong catalytic activity derived from the Co-N-C sites. Compared with the conventional synthetic method, the Co-N-C@carbon supports (Ketjen Black (KB), carbon nanotube (CNTs) and Super P) can be synthesized in a large scale and with much less cost through this strategy. The abundant Co-N-C species in Co-N-C @KB were proved to be ultimately conducive to the adsorption and conversion of polysulfides. Due to the structural and componential merits, the Co-N-C@KB can be used as an effective S host in Li-S batteries and demonstrate remarkable battery performance.

    In order to synthesize Co-N-C@KB, cobalt(Ⅱ) acetate (708 mg, 177.02 g·mol-1) and 2, 2'-bipyridine (1 874 mg, 156.19 g·mol-1) were firstly dissolved in 94 mL of ethanol, followed with stirring at 40 ℃ for 12 h. Secondly, KB (3 873 mg) was added to the solution and heated at 60 ℃ for 6 h in an oil bath under continuous magnetic agitation. The obtained dispersion was heated at 80 ℃ for 12 h to vaporize the ethanol until black powders were formed. The black powders were lightly ground with a mortar and pestle, and then transferred to an alumina crucible and placed in a tubular furnace. The furnace was therewith heated to 600 ℃ at a speed of 10 ℃·min-1 under Ar protection and then remained at 600 ℃ for 2 h to get the carbonized product Co-N-C @KB. The procedures of synthesizing Co-N-C@CNTs and Co-N-C@Super P were similar to Co-N-C@KB except for the replacement of KB with CNTs or Super P.

    Co-N-C@KB as well as the sublimated sulfur powders with the mass ratio of 2:7 was milled for 15 min in order to receive a homogeneous mixture. Next, the powder mixture was placed in the quartz tube and an annealing process was carried out in an argon atmosphere. The mixture was heated at 115 ℃ for 30 min and then heated at 155 ℃ for 12 h (2 ℃ ·min-1) to obtain the Co-N-C@KB/S powder. Co-N-C@Super P/S, Co-N-C@CNTs/S, KB/S, Super P/S and CNTs/S composites were prepared in a similar approach.

    First, an appropriate amount of sublimated sulfur and lithium sulfide (Li2S) (molar ratio of 5:1) were dissolved in 1, 3-dioxolane (DOL) and 1, 2-dimethoxy-ethane (DME) (1:1, V/V) solution and stirred on a mag-netic mixer for 24 h to obtain a 2 mmol·L-1 polysulfide solution. 20 mg of Co-N-C@KB was added to 4.0 mL polysulfide solution, and then the resulting mixture was vigorously stirred for 2 h and aged for 12 h. The sample status during the experiment was recorded.

    The active material Co-N-C@KB/S and polyvinylidene fluoride (PVDF) were ground at a mass ratio of 9:1 together with N-methyl pyrrolidone (NMP) to obtain an ink. The ink was then coated on aluminum foil and dried at 80 ℃ for 12 h. Afterwards, the active-material-coated aluminum foil was cut into small wafers, with the area of 1.13 cm-2. The area loading of S was between 1.5 and 2.0 mg·cm-2; the electrolyte on a single cell was about 60 μL. The battery was assembled in the form of 2032 coin-shaped cells, in which lithium metal foil was employed as the anode, with Celgard 2400 as the diaphragm and 1 mol·L-1 LiN(CF3SO2)2 (LiTFSI) in DME+DOL (1:1, V/V) with LiNO3 (mass fraction of 2%) as the electrolyte. All the battery assem-bling procedures were carried out in a glove box with less than 10-7 moisture and oxygen and the battery performance was evaluated by a LAND test system (Wuhan LAND Electronics Co., Ltd.). Cyclic voltammetry (CV) and AC impedance (EIS) were performed on CHI660E electrochemical workstation, with the sweep velocity of 0.1 mV·s-1 and the test voltage range of 1.7 ~2.8 V. EIS test ranged from 0.01 to 100 kHz with an amplitude of 10 mV.

    The crystal structure and phase composition of the obtained materials were tested by X-ray diffraction (XRD) using a Shimadzu X-ray diffractometer (XRD-6000) with the Cu radiation (λ =0.154 nm). The working current was 20 mA and working voltage was 40 kV with 2θ range of 10° ~80°. The morphology and microstructure of the materials were observed through scanning electron microscop (SEM, Quanta FEC 250, 10 kV), and transmission electron microscopy (TEM, JEM-1400plus, 100 kV) appliances. The S content was measured by a thermal analyzer (Setaram Labsys Evo) in an N2 atmosphere with a heating rate of 10 ℃·min-1 from room temperature to 600 ℃. Specific surface area and pore size distribution were tested by a specific surface analyzer (SA3100, Beckman Coulter). The elemental and chemical state information were analyzed with the X-ray photoelectron spectroscopy (XPS, AXIS-Ul-tra DLD). Raman spectroscopy was evaluated using the Renishaw inVia spectrometer.

    The working electrode was made of active materials (Co-N-C@KB/S), KB and polymer binder (polytetra-fluoroethylene, PTFE) in a weight ratio of 80:10:10. Ethanol was used as a solvent and added into the above mixture, for the formation of a black paste. The paste was coated onto an aluminum mesh to form an S-cathode, which was then dried at 80 ℃ for 12 h under the vacuum condition. The S-cathode and Li-anode were folded to form multideck electrodes in an Ar-protected glove box. Then, aluminum-plastic shells were used to pack the stacked electrodes. After that, electrolyte was added inside the battery through a vacuum injection machine. The electrolyte contains 1 mol·L-1 LiTFSI in DME+DOL (1:1, V/V) with LiNO3 (mass fraction of 2%). The mass ratio of electrolyte and sulfur was 4. At last, the aluminum plastics shells outside the electrodes were sealed by a heat-sealing device.

    The synthesis path of Co-N-C@KB/S is illustrated in Fig. 1. First, uniformly dispersed 2, 2'-bipyridine was used as a ligand, combining with cobalt(Ⅱ) acetate to form a metal complex, which would be absorbed on the KB. The surface-modified carbon was further pyrolyzed in argon at 600 ℃ to immobilize the Co species, leading to the production of Co-N-C@KB. Actually, with this method, a series of sulfur host materials with Co-N-C species on the carbon supports can be synthesized. The significant effect of Co-N-C@KB on anchoring of polysulfide can be proved by the adsorption test as exhibited in Fig. S1. Compared with the result of pure KB, a distinct adsorption phenomenon was found when Co-N-C@KB was added into the solution of Li 2Sn. This result indicates the strong adsorbing capability of Co-N-C@KB to capture lithium polysulfide.

    Figure 1

    Figure 1.  Schematic illustration of synthesis process and adsorption mechanism for Co-N-C@KB/S composite

    Physical and chemical characterization were used to reveal the structural and morphological characteristics. The morphologies of the three samples were characterized by SEM (Fig. 2a~2c), wherein there were no obvious particles present on the three carbon supports. There were similar morphologies for Co-N-C@KB and Co-N-C@Super P. Co-N-C@CNTs exhibited uniformly distributed tubes, which construct a multi-dimensional network, improving the electrical conductivity of the material and speeding up the transport of ions and electrons. The further analysis of the microstructure was characterized by TEM (Fig. S2a~S2c). The scanning transmission electron microscope (STEM) image and the EDS elemental mappings of Co-N-C@KB are dem-onstrated in Fig. 2d and 2e, wherein Co, N and O were homogeneously incorporated in the carbon support, illustrating that the carbon composites containing uniformly distributed Co-N-C species were successfully prepared. As can be exhibited through the high-resolution TEM (HRTEM) image of Co-N-C@KB in Fig. 2f, there was no crystalline lattice fringe present in the carbon support and the selected area electron diffraction (SAED) pattern (inset) showed no rings or bright spots, indicating very low crystallinity and no Co agglomeration. These results indicate that the Co-N-C were uniformly dispersed on the KB support.

    Figure 2

    Figure 2.  SEM images of (a) Co- N-C@KB, (b) Co-N-C@Super P and (c) Co-N -C@CNTs; (d) STEM image of Co-N-C@KB and (e) corresponding EDS elemental mappings; (f) HRTEM image and SEAD pattern (inset) of Co-N-C@KB

    The XRD patterns of Co-N-C@KB, Co-N-C@Super P, Co-N-C@CNTs and KB are displayed in Fig. 3a. It can be found that the broad peaks centered at around 24° and 44° correspond to the (002) and (100) planes of graphitic carbon. No metal-related peaks were observed in the XRD patterns, which is consistent with the TEM results. This result indicates that a low pyrolysis temperature of 600 ℃ prevents the formation of metal nanoclusters. Raman spectra are shown in Fig. 3b, wherein two significant carbon peaks at 1 341 cm-1 (D band) and 1 597 cm-1 (G band) correspond to the defective and graphitic structure, respectively. The ID/IG values of Co-N-C@KB and KB were 1.067 and 1.197, respectively, indicating the transformation of more amorphous carbon into graphitized carbon and ensuring the excellent conductivity of Co-N-C@KB. Nitrogen adsorption-desorption isotherms were collected to analyze the BET (Brunauer-Emmett-Teller) data of the composite, from which the pore-size distribution plots can be calculated with the Barrett-Joyner-Halenda (BJH) model. As shown in Fig. S3, all three samples showed the typical characteristics of high porosity. The BET specific surface areas of Co -N-C@KB, Co-N-C@ Super P and Co-N-C@CNTs were calculated to be 195, 60 and 226 m2·g-1, respectively. Noticeably, the high specific surface areas of Co-N-C@KB would efficiently improve the capability of ion exchange with electrolyte and adsorption for polysulfide, thus contributing to its outstanding discharge specific capacity and cycling stability. TGA (thermogravimetric analysis) test was carried out to measure the sulfur ratio in the S/C composite, thus verifying the hosting capability of the materials to sulfur. The TGA results of Co-N-C@KB, Co-N-C@Super P and Co-N-C@CNTs are shown in Fig. S4. The sample began to lose weight at about 200 ℃, and the most obvious weight-loss phenomenon appeared at about 300 ℃, indicating that a large amount of S in the sample escaped at this step.brrhzimage: 6:erhhzThe S contents of Co-N-C@KB, Co-N-C@Super P and Co-N-C@CNTs samples were determined to be mass fraction of 72.0%, 72.5% and 75.4% respectively, which are similar to the actual ratio of additions in the mixture. This result indicates that there was little S loss in the melting process and the Co-N-C modified carbon composites had a strong affinity to S.

    Figure 3

    Figure 3.  (a) XRD patterns and (b) Raman spectra of Co-N-C@KB, Co-N-C@Super P, Co-N-C@CNTs and KB; (c) XPS spectra of Co-N-C@KB, Co-N-C@Super P and Co-N-C@CNTs; (d~f) Co2p, C1s and N1s XPS spectra of Co-N-C@KB

    XPS analysis was used to further characterize the elemental composition of the samples. Fig. 3c shows the XPS survey spectra of Co-N-C@KB, Co-N-C@Super P and Co-N-C@CNTs, indicating that the four elements of Co, C, N and O are successfully incorporated in the carbon support. This result is in keeping with the EDS spectrum as displayed in Fig. S5. The Co contents in Co-N-C@KB, Co-N-C@Super P and Co-N-C@CNTs are displayed in Table S1, wherein the Co content of Co-N-C@KB was calculated to be atomic fraction of 0.58%. Fig. 3d exhibits the Co2p spectrum at the core level, wherein there were six peaks, matched to Co2p3/2, Co2p1/2 and satellite peaks, respectively. The peaks at 803.5, 796.2 and 792.1 eV correspond to the vibrating satellite peaks, Co2+ and Co3+ for Co2p1/2, and the other three peaks at 786.5, 781.1 and 779.4 eV correspond to the vibrating satellite peaks, Co2+ and Co3+ for Co2p3/2[14]. As displayed in Fig.S6, the XPS spectra of Co-N-C@Super P and Co-N-C@CNTs demonstrate similar results to that of Co-N-C@KB. The C1s spectrum of Co-N-C@KB is shown in Fig. 3e, wherein the main peak at 284.8 eV can be fitted to the typical C=C bond. In addition to the C=C bond, the peak at 290.4 eV matches the C—O bond, which might be derived from the partial oxidation of C in the air. The N1s spectrum of Co-N-C@KB is shown in Fig. 3f, in which the peaks at 401.7, 400.5, 399.6 and 399.4 eV correspond to graphitic-N, pyrrolic-N, Co—Nx and pyridinic-N, respectively[33]. The abundant Co—Nx and pyridinic - N would be helpful for the anchoring and conversion of the polysulfide[6]. In addition, the O1s spectrum was provided in Fig.S7, which shows two peaks at the binding energies of 532.9 and 534.5 eV, indicating the presence of oxygen ions in the Co-N-C@KB[34].

    The initial discharge/charge curves for Co-N-C@KB, Co-N-C@Super P, Co-N-C@CNTs, KB, Super P and CNTs at 0.05C are shown in Fig. 4a. The specific discharge capacities of Co-N-C@KB, Co-N-C@Super P and Co-N-C@CNTs were 1 216, 974 and 1 180 mAh· g-1 respectively, greater than that of KB, Super P and CNTs under the same condition. This result shows that the introduction of Co -N-C species on the carbon efficiently increases the reaction sites and enlarges the capacity of Li-S battery. The EIS spectra of Co-N-C@KB and KB are shown in Fig. 4b, to study the electron and ion transfer ability on the electrode interface. The charge-transfer resistance (Rct) of Co-N-C@KB in the high-frequency region was about 120 Ω, much less than that of KB, indicating Co-N-C@KB has a faster

    Figure 4

    Figure 4.  (a) Charge/discharge profiles of Co-N-C@KB, Co-N-C@Super P, Co-N-C@CNTs, KB, Super P and CNTs at 0.05C; (b) EIS spectra of Co-N-C@KB and KB; (c) CV curves of Co-N-C@KB and KB; (d) Charge/discharge profiles of Co-N-C@KB electrode at different current rates; (e) Rate capacities comparison between Co-N-C@KB and KB; (f) Cyclic performances of Co-N-C@KB and KB at 0.2C

    charge transfer rate on the cathode/electrode interface, indicating superior reaction kinetics to KB. The CV curves of Co-N-C@KB and KB electrodes were performed within the voltage range of 1.7~2.8 V at 0.1 mV·s-1. As shown in Fig. 4c, there were a couple of cathodic reduction peaks, as well as a couple of anodic oxidation peaks appearing at the symmetrical positions. For the Co-N-C@KB electrode, the reduction peak at about 2.32 V corresponds to the transition of S8 into long-chain polysulfide (Li2Sx, 4 ≤ x ≤ 8), and another peak at around 2.03 V corresponds to the conversion of the long-chain polysulfide into short-chain Li2 S and Li2S 2[35]. The two anodic peaks at 2.27 and 2.39 V correspond to the oxidation of short-chain Li2S2/Li2S to polysulfides and then to elemental sulfur[14]. Compared with the KB electrode, the Co-N-C@KB electrode undergoes distinguishable positive shift in the two cathodic peaks and remarkable negative shift in the anodic peaks. It is demonstrated that Co-N-C@KB can greatly decrease the electrochemical polarization and facilitate the polysulfide redox reaction kinetics. This result is consistent with the charge and discharge profiles in Fig. 4a and in-dicates better transformation ability of discharge/charge products on the Co-N-C@KB electrode. To evaluate the rate capability, we ran the Co-N-C@KB-based Li-S batteries under progressively enlarged current rates, ranging from 0.02C to 0.5C. The related charge/discharge profiles are shown in Fig. 4d, wherein the corresponding specific capacity recorded at 0.02C, 0.05C, 0.1C, 0.2C and 0.5C were 1 442, 1 216, 1 049, 858 and 623 mAh·g-1, respectively. Furthermore, the discharge capacities obtained at various current densities during the cycling discharge/charge tests were plotted as demonstrated in Fig. 4e, indicating that larger capacities at all the four current densities were achieved by Co-N-C@KB, compared with KB. When the current density returned to 0.1C, the specific capacity of the Co-N-C@KB -based battery recovered to 1 059 mAh·g-1, with a retention rate of nearly 95%, indicating a good rate capability of the Co-N-C@KB electrode. The cyclic stabilities of Co-N-C@KB and KB were evaluated through a galvanostatic cyclic discharging/charging process at the current density of 0.2C. As shown in Fig. 4f, the Co-N-C@KB-based Li-S battery showed a stable charge/discharge reversibility with a capacity retention rate of more than 72.5% up to 300 cycles. It was found that the Co-N-C@KB-based battery has higher retention rate of the discharge capacity in the whole 300 cycles in comparison with that of the KB-based counterpart. These results show that Co-N-C@KB can effectively facilitate the conversion of polysulfide and enhance the effective utilization of the cathode S, thus improving the discharge depth. For comparison, some reported transition metals-based carbon materials as the sulfur hosts and their related electrochemical performances are listed in Table S2[36-45]. Compared with the reported materials, the material in this work has some advantages in the initial discharge performance and cycle performance.

    The SEM images of Co-N-C@KB electrode before and after 300 discharge/charge cycles are given in Fig. 5a and 5b. There was no obvious change in the morphology of the KB particles. This result demonstrates the structural stability of Co-N-C@KB for the reversible charge-discharge processes. Fig. 5c shows the mass-preparation scale of Co-N-C@KB composite can be up to over 215 g for 10-time repetitive preparing procedures. As shown in Fig. 5d, the mass of as-synthesized active Co-N-C@KB composite is enough for preparing the necessary cathode marital of a soft-package Li-S battery (with a high surface loading of 23.8 mg·cm-2 on the cathode), whose size diagram is shown in Fig. S8. This battery can deliver a discharge capacity of 621 mAh and achieve a specific capacity of 1 042 mAh·g-1, indicating a potential for the application in high-capacity and large-size Li-S batteries.

    Figure 5

    Figure 5.  SEM images of Co-N-C@KB (a) before and (b) after 300 discharge/charge cycles; (c) Digital photograph for Co-N-C@KB synthesized in large scale; (d) Discharge curve and digital image (inset) of Co-N-C-@KB-based soft-pack Li-S battery

    To sum up, through utilizing the cost-effective ligand 2, 2'-bipyridine, a series of Co-N-C@carbon composites can be prepared. Specially, the Co-N-C@KB electrode combines the high conductivity, the high specific surface area of KB and abundant functional sites of Co-N-C species. The rich surface defects and active sites in Co-N-C@KB help to anchor the polysulfide and therewith catalyze its conversion, thus not only enhancing the utilization efficiency of S but also effectively inhibiting the shuttle effect. Due to the above advantages, the Co-N-C@KB electrode helps the Li-S battery to achieve a high initial capacity of 1 442 mAh·g-1 and excellent capability of capacity retention during the cyclic discharge/charge process. In addi-tion, this method could be applied to various kinds of transition metals, which can be effectively and uniformly supported on the carbon matrix. Therefore, this work paved a simple and economical way by modifying the conductive carbon materials with abundant transition metal atoms as the active sites to improve the performance of the chargeable Li-S battery.


    Acknowledgments: This work was funded by grants from the National Natural Science Foundation of China (Grants No. 21905139, 51902166). Meanwhile, this work was supported by Jiangsu Cyan Engineering of Higher Education, Priority Academic Program Development of Jiangsu Higher Education Institutions (PAPD), Jiangsu Joint Laboratory of Atmospheric Pollution Control, and Jiangsu Engineering Technology Research Center of Environmental Cleaning Materials. SONG Li and JIN YaChao were financially supported by Research Start-up Fund of NUIST. Supporting information is available at http://www.wjhxxb.cn
    Declaration of interests: The authors declare that there are no known competing financial interests or personal relationships that could have appeared to influence the work reported in this paper.
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  • Figure 1  Schematic illustration of synthesis process and adsorption mechanism for Co-N-C@KB/S composite

    Figure 2  SEM images of (a) Co- N-C@KB, (b) Co-N-C@Super P and (c) Co-N -C@CNTs; (d) STEM image of Co-N-C@KB and (e) corresponding EDS elemental mappings; (f) HRTEM image and SEAD pattern (inset) of Co-N-C@KB

    Figure 3  (a) XRD patterns and (b) Raman spectra of Co-N-C@KB, Co-N-C@Super P, Co-N-C@CNTs and KB; (c) XPS spectra of Co-N-C@KB, Co-N-C@Super P and Co-N-C@CNTs; (d~f) Co2p, C1s and N1s XPS spectra of Co-N-C@KB

    Figure 4  (a) Charge/discharge profiles of Co-N-C@KB, Co-N-C@Super P, Co-N-C@CNTs, KB, Super P and CNTs at 0.05C; (b) EIS spectra of Co-N-C@KB and KB; (c) CV curves of Co-N-C@KB and KB; (d) Charge/discharge profiles of Co-N-C@KB electrode at different current rates; (e) Rate capacities comparison between Co-N-C@KB and KB; (f) Cyclic performances of Co-N-C@KB and KB at 0.2C

    Figure 5  SEM images of Co-N-C@KB (a) before and (b) after 300 discharge/charge cycles; (c) Digital photograph for Co-N-C@KB synthesized in large scale; (d) Discharge curve and digital image (inset) of Co-N-C-@KB-based soft-pack Li-S battery

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  • 發布日期:  2021-06-10
  • 收稿日期:  2021-01-17
  • 修回日期:  2021-03-20
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