Sepiolite Enfolded Sulfur/ZnO Binary Composite Cathode Material for Li-S Battery

Lithium-Sulfur (Li-S) batteries have become an incredible challenge for the approaching age of high-vitality stockpiling gadgets. Nevertheless, one of the main specialized issues emerging in Li-S batteries is the polysulfide disintegration among electrodes and striking capacity limit. Here, sieved sepiolite (200 mesh sieve) has been favored as an added substance material to counter the above difficulties in the sulfur battery. The zinc oxide nanoparticles were prepared by co-precipitation method and a Sulfur/post-treated sieved Sepiolite/Zinc Oxide (S/PTSp/ZnO) nanocomposite was prepared by warmth treatment. The prepared composite was described by XRD, FTIR, RAMAN, SEM with EDAX, TEM, XPS, TG, and Electrochemical analysis. The S/PTSp/ZnO composite cathode exhibited an initial discharge capacity of 1,391 mAhg⁻¹ and attained a stable capacity of 765 mAhg⁻¹ at 200 cycles. In conclusion, Li-S batteries can be relied upon to capably build up the utilization of sulfur and limit the disintegration of polysulfides into an electrolyte.

Introduction

Sulfur offers one of the most noteworthy theoretical specific capacities (1,675 mAhg⁻¹) among all the metal oxides. The system could hypothetically deliver the energy density of 2,600 Wh kg⁻¹ (Bruce et al., 2012). In addition, sulfur is an inexhaustible component, non-dangerous, and incredibly modest, which makes it appealing for substantial scale applications (Ji and Nazar, 2010). A realistic target of practical energy density is in the range of 400–600 Wh kg⁻¹, which is higher when compared with the classical Li-ion batteries.

Li-S batteries are considered to be sensible for the generation of high-capacity energy storage devices.

However, there is still a long way to go and many challenges to overcome, since the system suffers from several unresolved drawbacks, which induce a large gap between reality and expectations. The major barriers to developing practical sulfur cathodes during the charge-discharge process include the highly insulating nature of sulfur, polysulfide dissolution, and volume expansion (Krishnaveni et al., 2018). The significant hindrances to the improvement of Li-S batteries are their low active material utilization rate, poor cycle life, and low coulombic efficiency (Evers and Nazar, 2013; Fu and Su, 2013). It is important to depict the method for how Li-S batteries work, as its mind-boggling working component is altogether different from the traditional Li-ion batteries. There are two basic strategies to conquer the above mentioned obstacles: (i) by coating the battery with metallic oxides and polymers; and (ii) by coating the battery with carbon materials, which could confine the sulfur or lithium polysulfides within the framework by using host materials (Radhika et al., 2018). A few methodologies have been connected to address the difficulties portrayed above, including the utilization of metal sulfides (Han et al., 2003), organic sulfides (Qiu et al., 2010; Wu et al., 2011), and metal oxides (Song et al., 2004; Zheng et al., 2006). Despite the fact that these techniques are helpful in improving the electrochemical performances, the security issues and sulfur as a functioning material can be utilized for electrode preparation. A conductive added substance is constantly added to the electrode, so as to give an electronic permeation to the entire electrode. Here post-treated sieved sepiolite acts as an additive material and it is well-matched for the establishment of a cathode material for Li-S batteries.

Sepiolite is a fibrous hydrated magnesium silicate clay mineral, having the elemental formula Mg₈Si₁₂O₃₀ (OH)₄(H₂O)₄·8H₂O. Like other silicate minerals, it contains a hysterically two-dimensional tetrahedral sheet but has no lasting octahedral sheets (Alvarez et al., 1984). In this manner, sepiolite has nano-sized channels containing water (Bokobza et al., 2004; Burzo and Wijn, 2009). The fibrous naturally visible high specific surface region, magnificent adsorption properties, rich micro- porosity, and low cost are additionally outstanding properties of the sepiolite material (Can et al., 2010; Fu et al., 2015; Zhang et al., 2015). Based on the above highlights, Sepiolite has been given significantly more focus in the world and many researchers are looking to use clay minerals in electrode material research.

ZnO nanopowders have been synthesized using various methods, such as Moezzi et al. (2012) the soft chemical method (Vayssieres, 2003), the sol-gel process (Zhang et al., 2003), the vapor phase growth (Sun et al., 2004), the co-precipitation method, and the vapor liquid-solid process (Gao and Wang, 2004), and so forth. Here, zinc oxide is a non-poisonous, n-type II-VI semiconductor material having a wurtzite structure with a direct and wide band gap of 3.37 eV. Its properties include close UV emanation, optical straightforwardness, great electrical conductivity, and piezoelectricity (Ozgur et al., 2005; Coleman and Jagadish, 2006). The improved electrochemical performance was observed due to the good electrode/electrolyte contact ensured by the large surface area of nanoscale particles (Muruganantham et al., 2016). Sulfur acts as an insulator; for that reason the additive material, such as post-treated sieved sepiolite, and metal oxide ZnO nanoparticles are used to improve the conductivity of the material in the Li-S batteries.

Materials and Methods

Sepiolite powders (Sp) were bought from a mineral processing factory in Sigma Aldrich, India. Sodium Hydroxide (NaOH), Sulfur (S), Zinc oxide (ZnO), Zinc Nitrate Hexahydrate [Zn (NO₃)₂·6H₂O], and Hydrochloric acid (HCl), were purchased from Axiom Chemicals Private Limited (India). All chemicals of analytical grade were used without further purification.

Synthesis of ZnO Nanoparticles

Zinc oxide nanoparticles were synthesized by a co-precipitation method using zinc nitrate and sodium hydroxide as a precursor. In this experimental work, the 0.4 M aqueous solution of zinc nitrate [Zn(NO₃)₂·6H₂O] was kept under constant stirring using a magnetic stirrer to completely dissolve the zinc nitrate for 1 h and 0.8 M of NaOH aqueous solution was added drop by drop slowly under high-speed constant stirring. The reaction was allowed to proceed for 2 h after completion. The beaker was sealed after 4 h. After the completion of the reaction, the solution was allowed to settle overnight and further, the supernatant solution was separated carefully. The remaining solution was centrifuged for 10 min, and the precipitate was removed. Thus, precipitates of ZnO nanoparticles were cleaned with de-ionized water three times and methanol was used to remove byproducts and then dried at about 80°C. Finally, dried Zn(OH)₂ was completely converted into ZnO nanoparticles (Maensiri et al., 2006).

Sepiolite Acid Treatment

Acid treatment was carried out using sieved sepiolite powder by adding 8 mole ratio of Hydrochloric acid and de-ionized water in a beaker without distressing at the surrounding temperature for 24 h. The clay minerals were filtered and washed with de-ionized water numerous times, and then dried at 40°C in a vacuum oven at 10⁻³ Torr for 12 h.

Thermal Activation Method

The post-treated sieved sepiolite powder is further proceeded with thermal activation method. In this process, eight mole ratios of post-treated sepiolite and ZnO nanoparticles were ball milled for 1 h at normal speed, and then the sample was manually mixed with sublimed sulfur (7:2:1) through fine grinding for 1 h and heated at 155°C for 20 h in a muffle furnace. The collected sample was milled and dried to attain the final product.

Characterization

The X-ray diffraction patterns and functional groups of calcined powder samples were inspected using X-ray Diffraction (PAN analytical XPERT-PRO with Cu-Kα radiation) and FTIR spectrometer recording IR spectra in the scope of 4,000–400 cm⁻¹ (Thermo Nicolet 380 Instrument Cooperation and KBr pellets). The morphology of the powders was reviewed by checking electron magnifying instrument (SEM FEG Quanta 250) and transmission electron magnifying lens (TEM) with vitality dispersive X-ray spectroscopy (EDS). The Thermogravimetric examination (TGA) estimations for the examples were done with a PerkinElmer Pyris Diamond TG/DTA warm analyzer in a nitrogen atmosphere with a warming rate of 10°C min⁻¹.

Electrochemical Performance

The positive electrodes comprised of 70 wt% of sulfur/sepiolite/ZnO composite, 20 wt% of acetylene black, and 10 wt% of polyvinylidene fluoride binders were homogeneously blended in an N-methyl-2-pyrrolidone (NMP) dissolvable and constantly ground for 3 h. The slurry was consistently coated on an aluminum foil, and after that dried at 60°C for 12 h. The CR2032 type coin cells were assembled in an argon-filled glove box, while lithium metal was utilized as a counter electrode and polypropylene layer was used as the separator in the Li-S battery. The electrolyte was prepared from 1,3-dioxolane, TEG (Tetra ethylene glycol), and DMG (dimethyl ether glycol). Electrochemical charge-release and cyclic performances were estimated at room temperature using a BTS-5V3A battery analyzer (Neware, Shenzhen, China), with the potential range from 3.0 to 1.0 V (vs. Li/Lis). Cyclic voltammetry (CV) and electrochemical impedance spectroscopy (EIS) were tested using a CHI660D electrochemical workstation (Chenhua, Shanghai, China) over a frequency range of 1 MHz to 0.1 Hz, with an open- circuit AC voltage amplitude of 5 mV.

Results and Discussion

The thermal stability of the Sulfur and as-arranged S/Sp/ZnO composites have been investigated by Thermo gravimetric analysis (TG) under N₂ atmosphere, as shown in Figure 1. At the point when the temperature increased, the mass of sulfur diminished to zero when it reached up to 315°C, and this is attributed to the complete melting of sulfur. Both TGA curves of sulfur and S/Sp/ZnO composite demonstrates the weight reduction stages from around 200 to 315°C, mirroring the evaporation of sulfur. The subsequent weight reduction of the composite is just about 65%, because of the vanishing of sulfur which is consistent with the added amount of proportions (Li et al., 2013; Yang et al., 2015).

FIGURE 1

Figure 1. TGA curves of (A) pure sulfur (B) S/Sp/ZnO.

The crystal structure of the as prepared sample was inspected by X-Ray Diffraction analysis and has been illustrated in Figure 2. The XRD pattern expressly shows that the as prepared zinc oxide has a leading peak at 2θ = 31.64, 34.36, 36.22, 47.55, 56.54, 62.79, 66.2° correlated to the Miller indices (100), (002), (101), (102), (110), (103), (112), respectively. This pattern is well in accordance with the hexagonal wurtzite period of ZnO (JCPDS Card No. 36-1451) through the sieved sepiolite reflection peak which appeared at 1.17 nm, relating to the (110) peak that was observed. Due to thermal treatment, the melting sulfur has very low viscosity and could easily disperse into the porous substrates. After the sulfur was integrated into the porous spaces, the sulfur was well-wrapped up into the composite material, which suggests that no sulfur envelops the outer surface of the composite (Rajkumar et al., 2018). The well-resolved sulfur peaks were scattered in the covering materials (Zegeye et al., 2016) and composites showed peaks of sulfur with decreased peak intensity when contrasted with the bare sulfur (JCPDS-Card No. 77-0145), demonstrating that sulfur is in the mesoporous sepiolite material.

FIGURE 2

Figure 2. XRD pattern of (A) SSp (seived sepiolite), (B) PS (sublimed sulfur), (C) ZnO (Zinc oxide nanoparticles), (D) S/SvSp/ZnO (sulfur/seived sepiolite/Zinc oxide), and (E) S/PTSp/ZnO (sulfur/post-treated seived sepiolite/Zinc oxide).

The functional groups of the FTIR spectra of S/PTSp/ZnO are as shown in Figure 3. There are several characteristic absorption peaks presented in the FT-IR spectra analysis. The bands at 1,108 cm⁻¹ are allocated to Si-O-Si (silanol group) in-plane vibration. In this way, these peaks could be utilized to confirm the sepiolite clay mineral. The peak at 467 cm⁻¹ is the characteristic absorption peaks of the wurtzite period of Zn-O. These results verify the event of Zn-O groups. 3,420 cm⁻¹ can be credited to the O-H stretching of the water. 2,927 cm⁻¹ are allocated to the C-H asymmetric stretching vibration. 1,636 cm⁻¹ are entrusted to the C=O extending vibration. The Si-O and O-H groups can be clearly observed in the FTIR of S/PTSp/ZnO.

FIGURE 3

Figure 3. FTIR spectra of (A) SSp, (B) ZnO, (C) S/SvSp/ZnO, and (D) S/PTSp/ZnO.

The Raman spectrums of sulfur, Zinc oxide, and S/PT Sp/ZnO have appeared in Figure 4. The E2 mode situated at 437 cm⁻¹ was observed for both compositions and showed the great crystallization nature of the wurtzite structure of ZnO nanoparticles. The band at 584 cm⁻¹ is related to E1 mode. It is commonly acknowledged that E1 is identified with the development of imperfections in the nanoparticles. The pure sulfur displays a characteristic peak at underneath 500 cm⁻¹, however here the peaks appeared nearly at 153, 218, and 475 cm⁻¹ which are started from the A1 symmetry mode of the S-S bond (Ward, 1968). Raman spectra of S/PTSp/ZnO quickens some vibrational signals beneath 500 cm⁻¹, showing that the sulfur is in a crystalline state. This outcome is in great agreement with the XRD results (Li et al., 2014).

FIGURE 4

Figure 4. Raman spectra of (A) sulfur, (B) ZnO, and (C) S/PT Sp/ZnO.

Figure 5 displays the N2 adsorption–desorption isotherms plot which confirms the porous structure of the composite material. The hysteresis loop of the PTSp/ZnO and S/PTSp/ZnO composite indicates that the sample is mesoporous in nature. The shape of the isotherm is linked with type 1 V isotherms with H3 hysteresis of the IUPAC classification. Based on DFT calculations, the pore size distribution is mainly focused at about 2–5 nm, which belongs to a mesoporous structure. The PTSp/ZnO sample exhibits a surface area of 320.5584 m²g⁻¹ and a pore volume of about 0.4 cm³g⁻¹, and also the S/PTSp/ZnO composite shows a specific surface of 172.603 m²g⁻¹ and a specific pore volume of 0.274 cm³g⁻¹. After sulfur impregnation, such a remarkable hysteresis loop was decreased and it was confirmed that the well distribution of sulfur particles had been embedded into the composite cathode material.

FIGURE 5

Figure 5. Nitrogen adsorption-desorption isotherms at 77 K of (A,C) PT Sp/ZnO and S/PT Sp/ZnO, (B,D) BJH pore size distribution of PT Sp/ZnO and S/PT Sp/ZnO.

SEM analyses were carried out for all composite materials to investigate the structure and morphology on the surface of sample. Figures 6A–C demonstrates the different magnifications of the SEM picture of PT Sp/ZnO and Figures 6D–F shows the SEM images of S/PTSp/ZnO. From that picture, the different sizes of unruffled sporadic porous particles are exhibited in an as-prepared sample. The morphology of sepiolite powders is composed of small micro fibrous porous bundles and, furthermore, ZnO nano-composites are placed as consolidated on the sepiolite structure. After sulfur was infused, the particles uniformly dispersed and observable aggregations appeared owing to thermal treatment (Figure S1).

FIGURE 6

Figure 6. SEM images of (A,B,C) PTSp/ZnO, (D,E,F) S/PTSp/ZnO.

The TEM micrographs can be seen from Figures 7A–D. The TEM picture demonstrates that the nanocomposite of Zinc oxide comprises of little round particles and a dark pole-like shape that corresponds to that sieved sepiolite powder, and that both are consolidated on the surface of sublimed sulfur. ZnO nanoparticles alone exceedingly and consistently mono dispersed on the sepiolite. This uniform scattering is in accordance with the smaller pore estimate appropriation of ZnO-N TEM images in figure. The fringes seen in Figure 7D explained the regular arrangement of atoms in the material.

FIGURE 7

Figure 7. TEM images of (A,B) PTSp/ZnO, (C,D) S/PTSp/ZnO.

XPS examinations have been employed from the survey of 0–1,250 eV to examine the S/PTSp/ZnO composite sample, which exposes the presence of Mg, Zn, O, C, S, and Si elements. The peaks are situated at 1304.5, 1022, 532.6, 285.4, 164.1, and 103.3 eV corresponding to Mg1s, Zn2p, O1s, Cls, S2p, and Si2p, respectively. Figure 8 shows the wide spectrum of the as prepared sample which is attributed to of S2p1/2, S2p3/2, Mg1s, Si2p, Zn2p3/2, and O1s. The peak appearing at 164.1 and 165.1 eV correspond to S2p3/2 and S2p1/2a bridge sulfur of the polysulfide species, which is likely to be created by means of the oxidation of sulfur upon heating (Kumar et al., 2017). The short chain sulfur (S2) and sulfide (S22-) peaks are attributed to the S2p spectrum. The short chain sulfur (S2) and sulfide (S22-) peaks are attributed to the S2p spectrum in the range of 166 to 172 eV. The peak located at 167.2 eV was ascribed to thiosulfate, which is formed due to polysulfide oxidation on the ZnO surface (Xu et al., 2015). The peak 1,022 eV committed to zinc oxide nanocomposite particle.

FIGURE 8

Figure 8. XPS (A) Wide spectrum of S/PTSp/ZnO composite, Spectra of (B) S2p1/2 and S2P3/2, (C) Magnesium, (D) Silica, (E) Zn2p3/2, (F) Oxygen.

Electrochemical Properties

The electrochemical mechanism of the as prepared composite lithium-sulfur battery was examined using cyclic voltammogram performances. Figure 9 illustrates the initial five cycles of the composite cathode material. The S/PTSp/ZnO composite reveals an anodic oxidation peak and two cathodic reduction peaks in the initial five cycles. These peaks are useful for a sulfur-based electrode. The two reduction peaks appearing at 2.29 and 2.0 V, where the peak around 2.29 V is attributed to the pure sulfur, changed over into long-chain multi-lithium sulfide (Li₂S_n, 4 < n <8), while 2.0 V convey to the arrangement of insoluble lithium sulfides (Li₂S₂/Li₂S), respectively (Sun et al., 2008; Ji et al., 2011). There is only one main sharp oxidation peak observed in the anodic scan at around 2.47 V, which indicates that multi lithium sulfide and Li₂S have oxidized into elemental sulfur. These outcomes endorse that there was no outstanding potential shift in the excellent electrochemical stability and also verifies the minimization of active loss in the as prepared sample and an improvement of reversibility of the anode with the cycling process.

FIGURE 9

Figure 9. Cyclic voltammetry curves of the S/PTSp/ZnO composite potential range from 1.5 to 3 V (verses Li⁺/Li).

Figure 10A shows the galvanostatic charge-discharge curves at different cycles for the S/PTSp/ZnO composite at a scan rate of 0.1 C with the potential range of 1.5–2.7 V. The specific capacity of the as prepared sample has been considered from the basis of sulfur mass (Lee et al., 2015). From the profile, it appears that there are two distinct discharge plateaus and one charge plateau was observed, which is consistent with the CV results (Zegeye et al., 2016). The initial specific discharge capacity of the S/PTSp/ZnO composite cathode material exhibits about 1,391 mAhg⁻¹ and it maintains a 765 mAhg⁻¹ at 200th cycle. The sepiolite and ZnO nanoparticles are favorable for restraining the polysulfides in the cathode and avoiding their dissolution into electrolytes. The discharge potential plateaus of the S/PTSp/ZnO composite cathode are stable up to 50 cycles, which indicates the good electrochemical performance of the prepared composite cathode. Figure 10B demonstrates the rate performance of the S/PTSp/ZnO composite material at different current densities. By cycling from low to high rates of 0.1, 0.2, 0.5, and 1 C, the composite electrode illustrated the charge capacities of 1,391, 1,110, 950, and 751 mAhg⁻¹. The excellent cycling stability and rate capability are confirmed from the as-prepared sample.

FIGURE 10

Figure 10. (A) Galvanostatic charge-discharge curves of 1st, 5th, 10th, 50th, 100th, 150th, and 200th cycle of the S/PTSp/ZnO composite at a scan rate of 0.1 C. (B) Rate performance of the S/PTSp/ZnO.

Figure 11 shows the cyclic performance of the S/PTSp/ZnO composite material at a stable density of 0.1 C. The coulombic efficiency of 99% was obtained from the as-prepared sample, which showed an excellent reversible electrochemical reaction and also attained a capacity retention of about 69%. The electrode material based on the high concentration of additive materials was used to recover the battery performance and also coulombic efficiency ensuring a drastically enhanced cycling stability, discharge capacity, and prevention of active material loss. As a result, the composite material exhibits a better performance due to a high content of additive sepiolite and metal oxide, which can strongly diffuse the polysulfide dissolution out of the electrode and improve the conductivity of the material.

FIGURE 11

Figure 11. Cyclic performance and the Coulombic efficiency of S/PTSp/ZnO Composites under discharge rate of 0.1 C.

Conclusion

To conclude, the Metal oxide ZnO nanoparticles were combined by co-precipitation technique and the sulfur/sepiolite/Metal oxide composite material was prepared using a simple heat treatment method. These examples were portrayed by XRD, FT-IR, RAMAN, TEM, XPS, TG, and SEM, examinations and electrochemical execution. All the diffraction peaks of the composites were in line with the standards. The functional vibrations of the as prepared composites were analyzed by FT-IR spectra. The fibrous morphology of the particles were observed by SEM images. In Raman spectra, below 500°C the sulfur and metal oxide peaks were obtained. TEM images clearly demonstrated the presence of sulfur, sepiolite, and ZnO nanoparticles. The above outcomes have clearly shown that the composite material is utilized to advance the great electrochemical execution of Lithium-sulfur batteries.

Data Availability Statement

The raw data supporting the conclusions of this article will be made available by the authors, without undue reservation.

Author Contributions

MS and RS: conceptualization, supervision, funding, methodology, investigation, formal analysis, original draft, review and editing, and project administration. CK: conceptualization, methodology, investigation, formal analysis, original draft, and review and editing. F-MW: conceptualization, funding, investigation, formal analysis, and review and editing.

Funding

All the authors acknowledge the financial support by DST-SERB, New Delhi under the Physical sciences, Grant sanctioned vide EMR/2016/006302. Also, all the authors acknowledge for the financial support by BSR of University grants Commission (UGC), FIST and PURSE programme of DST, New Delhi, India, and Ministry of Human Resource Development RUSA-Phase 2.0 Grant sanctioned vide Lt. No. F-24-51/2014U Policy (TN Multi Gen), Department of Education, Government of India.

Conflict of Interest

The authors declare that the research was conducted in the absence of any commercial or financial relationships that could be construed as a potential conflict of interest.

Supplementary Material

The Supplementary Material for this article can be found online at: https://www.frontiersin.org/articles/10.3389/fmats.2020.00109/full#supplementary-material

Figure S1. EDS analysis of the composite material.

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