key: cord-0022081-uwrsgj17
authors: Li, Huan; Meng, Rongwei; Guo, Yong; Chen, Biao; Jiao, Yan; Ye, Chao; Long, Yu; Tadich, Anton; Yang, Quan-Hong; Jaroniec, Mietek; Qiao, Shi-Zhang
title: Reversible electrochemical oxidation of sulfur in ionic liquid for high-voltage Al−S batteries
date: 2021-09-29
journal: Nat Commun
DOI: 10.1038/s41467-021-26056-7
sha: 1c5deb32378d889b9f3cdd09d301b9b94fb43ffb
doc_id: 22081
cord_uid: uwrsgj17

Sulfur is an important electrode material in metal−sulfur batteries. It is usually coupled with metal anodes and undergoes electrochemical reduction to form metal sulfides. Herein, we demonstrate, for the first time, the reversible sulfur oxidation process in AlCl(3)/carbamide ionic liquid, where sulfur is electrochemically oxidized by AlCl(4)(−) to form AlSCl(7). The sulfur oxidation is: 1) highly reversible with an efficiency of ~94%; and 2) workable within a wide range of high potentials. As a result, the Al−S battery based on sulfur oxidation can be cycled steadily around ~1.8 V, which is the highest operation voltage in Al−S batteries. The study of sulfur oxidation process benefits the understanding of sulfur chemistry and provides a valuable inspiration for the design of other high-voltage metal−sulfur batteries, not limited to Al−S configurations.

S ulfur is a promising electrode material in metal-sulfur batteries due to its earth abundance and high theoretical capacity [1] [2] [3] [4] [5] [6] . Sulfur is normally coupled with metal anodes and is electrochemically reduced with metal cations to form metal sulfides 7, 8 . Despite high specific capacities based on sulfur reduction, the reverse oxidation of these sulfides back to sulfur needs to overcome a high energy barrier 9,10 , leading to a large overpotential and poor reversibility. Additionally, the reduction of sulfur occurs at low electrochemical potential (~−1.0 V vs. standard hydrogen electrode, Fig. S1 ), and results in low operation voltage of metal-sulfur batteries 5, 6 . For example, Al-S batteries based on sulfur reduction usually demonstrate ultralow cell voltage of about~0.5 V 11, 12 . Therefore, the limited reversibility and low electrochemical potentials are the main obstacles for the practical use of sulfur electrodes.

Many efforts have been devoted toward improving the reversibility of metal-sulfur batteries by proper designs of sulfur host and electrolyte engineering 5, 6, [13] [14] [15] . However, these prior attempts failed to basically address the low-voltage concerns of metal-sulfur batteries because the cell voltage is determined by the redox pathway of sulfur but these efforts did not alter the sulfur reduction path. Therefore, the batteries based on the sulfur reduction remain far from satisfactory for the high-voltage applications [5] [6] [7] [8] [16] [17] [18] . It is highly important to examine new redox pathways of sulfur to achieve viable applications of metal-sulfur batteries. In this regard, sulfur oxidation is a worthy path because it can compensate the intrinsic low-voltage shortcoming of sulfur reduction.

Considering the multivalent nature of sulfur element (−2, 0, +2, +4, +6), sulfur can be oxidized into high-valence sulfur compounds 19, 20 . Unfortunately, the oxidation process of sulfur has been rarely studied. Due to the inert nature of sulfur, a high voltage needs to be applied to drive its electrochemical oxidation. This is normally accompanied by electrolyte decomposition, leading to a poor reversibility [21] [22] [23] . Meanwhile, the electrochemical oxidation of sulfur undergoes an electron-loss process involved with anions. The common anions in metal-sulfur batteries such as bis (trifluoromethyl) sulfonate, hexafluorophosphate are weak oxidants, which are not able to oxidize sulfur into high-valence sulfur compounds 24, 25 . Therefore, anions with strong oxidizing power in an electrochemically stable electrolyte are necessary to oxidize sulfur in a highly reversible manner, but this concept has not been explored yet.

In this work, we demonstrate, for the first time, the reversible sulfur oxidation in AlCl 3 /carbamide ionic liquid. The AlCl 4 − anions can oxidize sulfur to form aluminium sulfide chloride (AlSCl 7 ), which can be reversibly reduced back to sulfur with a high efficiency of~94%. This oxidation-reduction process is workable within a wide range of high electrochemical potentials. Benefiting from the high reversibility and high electrochemical potential, the Al-S battery can run steadily over 200 cycles around~1.8 V, which is the highest operation voltage in Al-S batteries reported so far. By sharp contrast, the previously studied Al-S battery based on sulfur reduction can only run tens of cycles with a much lower operation voltage of~0.5 V. This work sheds new light on the understanding of sulfur chemistry and presents sulfur oxidation as a new pathway to achieve the high-voltage applications of metal-sulfur batteries.

Evolution of AlSCl 7 during electrochemical sulfur oxidation. AlSCl 7 is an ionic crystal with SCl 3 + cations and AlCl 4 − anions 26 . AlCl 3 /carbamide ionic liquid contains AlCl 4 − , Al 2 Cl 7 − anions, and [AlCl 2 (carbamide) n ] + cations 27, 28 . Al anode demonstrates high reversibility and stable electrochemical potential in AlCl 4 − and Al 2 Cl 7 − containing electrolyte, and therefore Al anode is used as the reference electrode in this work [29] [30] [31] [32] . Figure 1a shows the linear scanning voltammetry (LSV) curve for sulfur/carbon nanotube (S/CNT) composite cathode with 10 wt.% polyvinylidene difluoride (PVDF) binder in AlCl 3 /carbamide electrolyte (Fig. S2 ). It should be noted that sulfur is not stable under high oxidation voltage in the commonly used AlCl 3 /1-ethyl-3methylimidazolium chloride electrolyte (Fig. S3 ). The sulfur content in S/CNT is 20 wt.% and the molar ratio of AlCl 3 to carbamide is 1.3:1 (details in the "Methods" section). The observed current densities in Fig. 1a are above~2.0 V and below 1.0 V, corresponding to the electrochemical oxidation and reduction of sulfur, respectively. Figure 1b summarizes the electrochemical potentials of different materials, and the potential of sulfur oxidation in this work is much higher than most of the previously reported materials (Table S1) 11, 12 . Cyclic voltammetry (CV) curves are compared to demonstrate the overall process of sulfur oxidation and reduction. The electrochemical oxidation from sulfur to AlSCl 7 starts from~2.0 V, and the reverse reduction from AlSCl 7 to sulfur occurs at~1.8 V (Fig. 1c) . For the sulfur reduction (Fig. 1d) , sulfur starts to be reduced to sulfides below~1.0 V. The electrochemical potential of sulfur oxidation is much higher than that of reduction. The potential difference is clearly seen in the galvanostatic charge-discharge curves. The sulfur oxidation presents obviously high discharge voltage plateau of~1.8 V (Fig. 1e) . However, the reduction of sulfur only shows a much lower operation voltage of~0.5 V (Fig. 1f) . To detect the phase evolution during the oxidation and reduction process, we carried out the in situ synchrotron-based X-ray diffraction (XRD) upon charge and discharge (Fig. 1g, h) . The elemental sulfur, Al 2 S 3 , and AlSCl 7 are orthorhombic, hexagonal, and monoclinic crystals with space groups of Fddd, P6 1 , and Pc, respectively (Fig. S4 ). During sulfur oxidation process, the orthorhombic sulfur transforms to the monoclinic AlSCl 7 , while during reduction process, sulfur is reduced to hexagonal Al 2 S 3 . Specifically, for sulfur oxidation process (Fig. 1g) , the peaks assigned to the (102), (013), and (110) facets of AlSCl 7 sequentially appear when the Al-S battery is charged to 2.4 V. For the reverse process from AlSCl 7 to sulfur, those peaks assigned to AlSCl 7 gradually disappear, and only the characteristic peaks of sulfur remain. It should be noted that the diffraction peak at 10.8°is assigned to the characteristic peak of sulfur and it remains during charge-discharge due to the incomplete electrochemical oxidation of sulfur. The above evidence confirms the efficient electrochemical oxidation of sulfur to AlSCl 7 , and the reversibility from AlSCl 7 back to sulfur. During sulfur reduction process (Fig. 1h) , the (011) and (016) diffraction peaks of Al 2 S 3 appear at 8.5 o and 16.6 o , respectively. For the reverse charge process, these peaks gradually disappear due to the conversion of Al 2 S 3 to sulfur. However, the (100) and (016) characteristic peaks of Al 2 S 3 can be also found during the charge process, which is due to the difficulty of reversible decomposition of Al 2 S 3 to sulfur. Both AlSCl 7 and Al 2 S 3 are also verified by the XRD plots at different cut-off voltages (Fig. S5) . The above evidence confirms sulfur oxidation and reduction chemistry, which is based on the AlSCl 7 and Al 2 S 3 products, respectively.

A direct view of these products is shown on the scanning transmission electron microscopic (STEM) images after charging the sulfur cathode at 2.4 V and discharging at 0.2 V. S 8 octamer is visible on the TEM image of pristine sulfur (Fig. S6 ). After electrochemical S reduction at 0.2 V (Fig. 2a) , a crystallized structure is seen with ( 114) Table S2 , and their optimized structures are shown in Fig. S9 . The details for determination of the Gibbs free energy are specified in the "Theoretical computations" part. For the sulfur oxidation process (Fig. 3a) , AlCl 4 − oxidizes S into AlSCl 7 solid accompanied by the loss of electrons (Eq. 1). Meanwhile, Al 2 Cl 7 − is reduced into AlCl 4 − with Al plated on Al anode. The change in the Gibbs free energy (ΔG) can be calculated by using the electron-transfer numbers (n) and the difference in the electrochemical potential (ΔU). With single-electron transfer, the difference in ΔG between cathode and anode is the operation voltage 33 . As expected, the sulfur oxidation demonstrates a high voltage of~1.76 V, which is consistent with the experimental observations of~1.8 V (Fig. 1c) .

For the sulfur reduction process, sulfur is reduced by Al 2 Cl 7 − cations to form Al 2 S 3 (Eq. 2), and meanwhile, AlCl 4 − etches Al anode to form Al 2 Cl 7 − . The voltage based on sulfur reduction is only~0.87 V (Fig. 3b) , much lower than that of sulfur oxidation. Additionally, the reverse reduction from AlSCl 7 to S only needs to overcome an energy barrier of 0.52 eV as calculated by the uphill of red lines in Fig. 3a . However, the energy barrier from Al 2 S 3 to S is as high as 3.98 eV (blues lines in Fig. 3b ). This comparison suggests the ease of reverse conversion from AlSCl 7 to S and therefore better reversibility of the sulfur oxidation-reduction process. Figure 3c , d schematically compares the sulfur oxidation and reduction process. The AlCl 4 − and Al 2 Cl 7 − anions serve, respectively, as the oxidizing and reducing agents reacting with sulfur, and Al anode is used as referenced electrode to pair with these redox reactions for charge balance.

We have summarized the pathways of sulfur oxidation and reduction as follows:

Sulfur oxidation:

Sulfur reduction:

Track of reaction intermediates via spectroscopic analysis. We combined synchrotron-based near-edge X-ray absorption fine structure (NEXAFS) spectra, X-ray photoelectron spectra (XPS), and in situ Raman spectra to identify the reaction intermediates during the sulfur oxidation process. As shown in the S K-edge NEXAFS spectra (Fig. 4a) , the characteristic peak of sulfur located at~2472 eV presents an obvious positive shift with higher voltage from open circuit potential (OCP) to 2.4 V. The shifted peak position of oxidation products from 2.2 to 2.4 V is nicely located between the peaks of 0-valence and +6-valence sulfur as compared to the reference samples of elemental sulfur, N 2 S 2 O 3 , and Li 2 SO 4 . This suggests the efficient oxidation of sulfur to higher valence at high voltages 34 . The positive shift of Cl characteristic peak is also identified from the Cl L-edge spectra at~201.3 eV (Fig. 4b) . This is attributed to the formation of S-Cl bonds in AlSCl 7 . The electronegativity of S is stronger than Al, and therefore the photon energy of Cl atoms among Cl-S bonds is higher than those among Cl-Al bonds 35 . By contrast, there is no peak shift for Al characteristic peak because the chemical state of Al remains unchanged during the sulfur oxidation process (Fig. S10) . To quantify the sulfur valence during its oxidation, we carried out the XPS measurement at different oxidation voltages (Fig. 4c) . According to the S 2p XPS spectra, peaks located at 169.4 and~168.3 eV gradually appear between the +2 thiosulfate and +6 sulfate 36 . These doublets are assigned to the +4 sulfur, confirming the stable presence of AlSCl 7 oxidized products. To detect the oxidation intermediates, we further carried out in situ Raman spectra measurement (Fig. S11) 37 . As shown in Fig. 4d , Raman peaks located at~145,~210, and 462 cm −1 are assigned to sulfur (Fig. S12) 38 . During the charging process, the intensity of these peaks gradually weakens, indicating the conversion from sulfur to AlSCl 7 . For the reverse process, these Raman peaks of sulfur reappear, which is a strong evidence of the high reversibility of sulfur oxidation. Notably, a new peak located at 530 cm −1 emerges (Fig. 4e) , which is attributed to the vibration of SCl 3 + cations 39 . These cations are soluble in the electrolyte, which may trap into separator and shuttle to Al anode. Therefore, the sulfur valence and reversibility are well characterized by spectroscopic analysis. AlSCl 7 tends to decompose to AlCl 4 − and SCl 3 + intermediates, leading to the loss of sulfur during electrochemical cycling.

High-voltage Al-S batteries based on sulfur oxidation. To demonstrate the possible application of sulfur oxidation, we assembled Al-S batteries based on the oxidation and reduction process and compared their operation voltages and cyclic stability. Al-S batteries were assembled with S/CNT cathode, Al referenced anode, AlCl 3 /carbamide ionic liquid, and a glass fiber separator using a 2032-coin cell type (more details in the "Electrochemical tests" section). The specific surface area of the cathode with 20 wt.% S in S/CNT composite is 154 m 2 g −1 (Fig. S13) . As shown in Fig. 5a , Al-S batteries based on the sulfur oxidation (AlSCl 7 product) run steadily over 200 cycles with a highest specific capacity of 225 mAh g −1 (Fig. S14) . Reversible redox reactions are defined as a pair of oxidation-reduction reactions with high reversibility. Coulombic efficiency (CE%) is a good parameter to describe the reversibility of electrochemical reactions on the electrodes in batteries. In this work, CE% is defined as the percentage ratio of the specific discharge capacity to the charge capacity. For Al-S batteries based on the sulfur oxidation, the CE% stabilizes as high as~94% upon cycling. This is ascribed to the efficient electrochemical oxidation of sulfur to AlSCl 7 and then highly reversible reduction from AlSCl 7 back to sulfur. However, it should be noted that the Al-S battery based on the sulfur oxidation also exhibits capacity decay upon long cycles. This is attributed to the gradual dissolution of SCl 3 + into the electrolyte (as evidenced by the in situ Raman spectra), leading to the loss of active sulfur (Figs. S15 and S16). Future work needs to be carried out to restrain the dissolution of SCl 3 + for more stable cycling performance. For the previously studied batteries based on sulfur reduction with Al 2 S 3 product, the sulfur cathode showed an ultrahigh specific capacity over 1000 mAh g −1 at the first cycle. However, it dramatically declined after tens of cycles due to the irreversibility (Fig. 5b) [40] [41] [42] . Figure 5c , d shows a comparison of the charge-discharge curves at different cycles. The Al-S battery based on the sulfur oxidation exhibits a high voltage of~1.8 V, and the voltage plateau remains stable during cycling. However, the Al-S batteries based on the sulfur reduction feature a much lower voltage of~0.5 V with severe voltage decline and capacity decay. Additionally, the Al-S battery based on the sulfur oxidation demonstrates high-rate performance. The sulfur cathode still has a high specific capacity of 120 and 95 mAh g −1 at 0.5 and 1 A g −1 , respectively (Fig. S17) . The Al-S battery maintains stable cycling at high current densities (Figs. S18 and S19). However, it is noteworthy that the specific capacity of sulfur decreases with higher sulfur contents and areal mass loadings (Figs. S20 and S21). Therefore, more attention should be paid in future on the design of sulfur host to improve the sulfur utilization with sulfur oxidation process. Despite the above advantages of Al-S batteries, we should also evaluate their pros and cons. The maximized energy density based on the active sulfur is estimated at~405 Wh kg −1 considering a specific capacity of 225 mAh g −1 with an average voltage plateau of~1.8 V at the beginning cycles. However, it should be noted that this value decreases upon battery cycling, and the energy density will be also compromised while considering the practical devices, including Al anode, electrolyte, separator, cell case, etc. Further work still needs to be carried out to optimize the energy density by improving the sulfur utilization and the areal mass loading of sulfur while decreasing the dosage of non-active parts. In addition, another advantage of Al-S battery is the low cost of electrode materials such as sulfur, Al, and the AlCl 3 /carbamide electrolyte ( Fig. S22 and Table S3 ). However, it should be also noted that the carbon nanotubes used in this work raise concerns about the cost-effectiveness. In the future works, it would be highly desirable to explore low-cost carbon or noncarbon hosts with lower cost and higher sulfur utilization.

We have demonstrated that sulfur can be electrochemically oxidized in ionic liquid with high reversibility. The reaction pathways, AlSCl 7 oxidized products, and SCl 3 + intermediates are well confirmed by means of in situ synchrotron-based analysis, highresolution microscopic images, spectroscopic analysis, and theoretical computations. The electrochemical oxidation from sulfur to AlSCl 7 is highly reversible with a stable CE% of~94%, and the oxidation process is workable within a wide range of electrochemical potentials. As a result, the Al-S battery based on sulfur oxidation process can run steadily over 200 cycles around~1.8 V, which is the highest operation voltage for Al-S batteries. It is expected that the sulfur oxidation process can be coupled with other metal anodes for various metal-sulfur batteries, not limited to Al-S batteries. This work sheds new light on sulfur chemistry and shows a great advantage of the sulfur oxidation pathway for the design of viable high-voltage metal-sulfur batteries.

Preparation of S/CNT cathode and AlCl 3 /carbamide ionic liquid. The S/CNT material was prepared by mixing sublimed S with CNT under 155°C for 12 h. Different sulfur contents in S/CNT can be achieved by adjusting the relative mass ratio of S and CNT. In all, 20, 40, and 80 wt.% of sulfur were used in this work. The S/CNT cathode was prepared by mixing S/CNT material with PVDF binder with a mass ratio of 90:10. The AlCl 3 /carbamide ionic liquid was synthesized by mixing AlCl 3 and carbamide with a molar ratio of 1.3:1. Specifically, AlCl 3 was gradually added into carbamide with continuous stirring in an Ar-filled glove box at the room temperature. During this process, these two solids melt with each other into liquid and finally form ionic liquid containing AlCl 4 − , Al 2 Cl 7 − , and [AlCl 2 (carbamide) n ] + .

Characterization of materials. The morphology and structure of the samples were characterized by scanning electron microscopy (Hitachi S4800, Japan). Highresolution TEM and STEM images were obtained by JEM-ARM200F TEM. XPS spectra were measured with the Thermo Fisher Scientific ESCALAB Xi+, Al Kα radiation. NEXAFS of S K-edge and Cl L-edge were performed on the soft X-ray spectroscopy beamline at Australian synchrotron (Clayton) AS, part of ANSTO. In situ synchrotron XRD data were collected on the powder diffraction beamline at the Australian Synchrotron with a wavelength of 0.6868 and 0.7290 Å. Data were collected continuously in 30 s acquisitions with coin cells. For sulfur oxidation, first the cells were charged at 0.2 A g −1 to 2.4 V and then discharged to 1.0 V. For sulfur reduction, first the cells were discharged to 0.5 V and then charged to 1.8 V at 0.5 A g −1 . The cell cases on both the negative and positive sides together with the Al foil anode were punched with d = 0.2 cm holes, and polyimide films were used to seal the holes but allowed the X-ray transmission. In situ Raman spectra were collected with Labram HR Evolution (Horiba scientific).

Electrochemical tests. For the assembly of Al-S batteries, the as-prepared S/CNT electrodes with different sulfur contents were coupled with an Al foil reference anode (100 μm thickness). These two electrodes were sandwiched by a glass fiber separator (GF/A) with AlCl 3 /carbamide ionic liquid (~140 μL). These components were placed into a 2032-coin cell configuration for further electrochemical tests. The LSV curves were scanned from OCP (≈1.4 V) at 0.5 mV s −1 . CV was carried out from 1.0 to 2.4 V for sulfur oxidation and from 0.2 V to 1.8 V for sulfur reduction. Data of LSV and CV curves were collected on an IVIUM electrochemical workstation. Galvanostatic charge-discharge cycles were performed at different current densities using a Neware battery tester. Theoretical computations. Computations for this work were carried out using DFT as implemented in VASP code. Electronic exchange-correlation energy was modeled using the Perdew-Burke-Ernzerhof function within a generalized gradient approximation. The projector-augmented wave method was used to describe the ionic cores. For the plane-wave expansion, a 450 eV kinetic energy cut-off was used following testing a series of different cut-off energies. Convergence criterion for the electronic structure iteration was set to 10 −4 eV and that for geometry optimization was 0.01 eV Å −1 on force. A Gaussian smearing of 0.1 eV was applied during geometry optimization and for total energy computations.

The Gibbs free energy was calculated based on the DFT-based energy (E), zeropoint energy (ZPE), and the entropy (TS) by using the following expression:

The change in the Gibbs free energy (ΔG) can be calculated by using the electron-transfer numbers (n) and the difference in the electrochemical potential (ΔU).

The difference in ΔG between cathode and anode is the cell operation voltage with single-electron transfer (n = 1).

The data that support the findings of this study are available from the corresponding author upon reasonable request.

Received: 18 June 2021; Accepted: 16 September 2021;

Nanostructured sulfur cathodes

A fundamental look at electrocatalytic sulfur reduction reaction

A high-energy and long-cycling lithium-sulfur pouch cell via a macroporous catalytic cathode with double-end binding sites

Initiating a reversible aqueous Zn/sulfur battery through a "liquid film

Nonlithium metal-sulfur batteries: steps toward a leap

A progress report on metal-sulfur batteries

A stable room-temperature sodium-sulfur battery

A rechargeable Al/S battery with an ionic-liquid electrolyte

Burning lithium in CS 2 for high-performing compact Li 2 S-graphene nanocapsules for Li-S batteries

Catalytic oxidation of Li 2 S on the surface of metal sulfides for Li-S batteries

Paving the path toward reliable cathode materials for aluminum-ion batteries

Emerging nonaqueous aluminum-ion batteries: challenges, status, and perspectives

Advances in lithium-sulfur batteries based on multifunctional cathodes and electrolytes

The rechargeable aluminum battery: opportunities and challenges

Designing host materials for sulfur cathodes: from physical confinement to surface chemistry

Surface-enhanced redox chemistry of polysulphides on a metallic and polar host for lithium-sulphur batteries

Selective catalysis remedies polysulfide shuttling in lithiumsulfur batteries

Surface chemistry in cobalt phosphide-stabilized lithiumsulfur batteries

Green chemistry and polymers made from sulfur

Sulfur chemistry in polymer and materials science

Structure and compatibility of a magnesium electrolyte with a sulphur cathode

Water-in-salt" electrolyte enables high-voltage aqueous lithiumion chemistries

Nonaqueous liquid electrolytes for lithium-based rechargeable batteries

Liquid electrolyte lithium/sulfur battery: fundamental chemistry, problems, and solutions

A review on the features and progress of dual-ion batteries

SCl 3 + AlCl 4 − : improved synthesis and characterization

High Coulombic efficiency aluminum-ion battery using an AlCl 3 -urea ionic liquid analog electrolyte

Using an AlCl 3 /urea ionic liquid analog electrolyte for improving the lifetime of aluminum-sulfur batteries

An ultrafast rechargeable aluminium-ion battery

A new aluminium-ion battery with high voltage, high safety and low cost

Suppressing Al dendrite growth towards a long-life Al-metal battery

Graphene nanoribbons on highly porous 3D graphene for high-capacity and ultrastable Al-ion batteries

Design of electrocatalysts for oxygen-and hydrogen-involving energy conversion reactions

Vulcanization reaction of squalene and S 8 powder studied by sulfur K-edge NEXAFS under liquid phase

HCl adsorption on ice at low temperature: a combined X-ray absorption, photoemission and infrared study

A highly efficient polysulfide mediator for lithium-sulfur batteries

Revealing principles for design of lean-electrolyte lithium metal anode via in-situ spectroscopy

In-situ Raman investigation of polysulfide formation in Li-S cells

Preparation, Raman and nuclear quadrupole resonance data for the complex SCl 3 + AlCl 4 −

room-temperature aluminum-sulfur batteries with a lithium-ion-mediated ionic liquid electrolyte

A novel non-aqueous aluminum sulfur battery

An aluminum-sulfur battery with a fast kinetic response

This research is financially supported by Australian Research Council (ARC) through Discovery Project Program (FL170100154, DP160104866). The team from Tianjin University thanks the National Natural Science Foundation of China (No. 51932005). DFT computations were undertaken with the assistance of resources and services from the National Computational Infrastructure (NCI) and Phoenix High Performance Computing, which are supported by the Australian Government and The University of Adelaide. This research was undertaken on the powder diffraction beamline and soft X-ray spectroscopy beamline at the Australian Synchrotron, Clayton, Victoria, a part of ANSTO. We thank Dr. Qinfen Gu at the Australian Synchrotron for help with synchrotron XRD experiments.

The authors declare no competing interests.

Supplementary information The online version contains supplementary material available at https://doi.org/10.1038/s41467-021-26056-7.Correspondence and requests for materials should be addressed to Shi-Zhang Qiao.Peer review information Nature Communications thanks Zhifeng Ding, Enyuan Hu, and the other anonymous reviewer(s) for their contribution to the peer review of this work.

Publisher's note Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.Open Access This article is licensed under a Creative Commons Attribution 4.0 International License, which permits use, sharing, adaptation, distribution and reproduction in any medium or format, as long as you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons license, and indicate if changes were made. The images or other third party material in this article are included in the article's Creative Commons license, unless indicated otherwise in a credit line to the material. If material is not included in the article's Creative Commons license and your intended use is not permitted by statutory regulation or exceeds the permitted use, you will need to obtain permission directly from the copyright holder. To view a copy of this license, visit http://creativecommons.org/ licenses/by/4.0/.