Method for regulating interlayer spacing of molybdenum disulfide layer by oxygen doping and application thereof

Abstract

The application discloses a method for regulating and controlling interlayer spacing of molybdenum disulfide by oxygen doping and application thereof, and belongs to the technical field of battery materials. The method comprises the following steps: pretreating carbon cloth; dissolving ammonium molybdate tetrahydrate and thiourea in deionized water to obtain a mixed solution; and performing hydrothermal reaction on the mixed solution and the pretreated carbon cloth to obtain oxygen-doped molybdenum disulfide grown in situ on the carbon cloth. Oxygen doping is introduced into the molybdenum disulfide, so that the interlayer spacing of the molybdenum disulfide is expanded, and the embedding / extraction kinetics of zinc ions and the structural stability are significantly improved. The capacity retention rate of the water-based zinc ion battery anode material prepared by the O-MoS2@CC material reaches 96.3% after 3000 cycles at a current density of 0.5 A g ‑ 1, and the water-based zinc ion battery anode material exhibits excellent cycle stability and rate performance compared with conventional MoS2@CC materials. The application has the advantages of simple process, strong controllability, suitability for large-scale production, provision of a new doping regulation strategy for design of high-performance water-based zinc ion battery anode materials, and important scientific significance and practical application value.

Description

Technical Field

[0001] This invention relates to a method and application for controlling the interlayer spacing of molybdenum disulfide through oxygen doping, belonging to the field of battery material application technology. Background Technology

[0002] The energy crisis and environmental pollution are becoming increasingly severe, seriously hindering global sustainable development. Against this backdrop, developing efficient and reliable electrochemical energy storage technologies to achieve efficient energy storage and stable output is a critical technological issue that urgently needs to be addressed in the energy sector.

[0003] Lithium-ion batteries, as the mainstream electrochemical energy storage device, have been widely used in portable electronic devices and electric vehicles. However, the increasing scarcity of lithium resources limits their application prospects in large-scale energy storage. Furthermore, organic electrolytes pose safety hazards such as flammability and decomposition, and their assembly conditions are stringent, further hindering their development. Therefore, the development of novel, highly safe aqueous battery systems is imperative.

[0004] MoS2, with its unique layered structure and tunable interlayer spacing, has shown broad application prospects in the field of energy storage and conversion, and has been widely explored as an electrode material for lithium / sodium-ion batteries. However, it faces severe challenges when used in aqueous zinc-ion batteries: the interlayer spacing of MoS2 is small, about 0.62 nm, which makes zinc ion insertion difficult, electrode polarization severe, specific capacity low and cycle performance poor.

[0005] To address the aforementioned issues, increasing the interlayer spacing of MoS2 has been proven to be an effective means of enhancing zinc ion storage capacity. Appropriate interlayer spacing expansion can improve the zinc ion storage capacity of Zn. 2+ Providing more insertion sites promotes ion diffusion and improves electrochemical performance. Current research has proposed strategies such as vacancy construction, phase-engineered recombination, and the introduction of water of crystallization to control interlayer spacing. For example, Wang et al. used defect engineering to make MoS2... 2-x At 0.1 A g -1 The capacity has been increased to 128 mAhg -1 Kang et al. successfully expanded the interlayer spacing of MoS2 by using water of crystallization to improve the cycling and rate performance of MoS2 nanosheets; however, these modification methods still failed to completely solve the problem of volume expansion caused by zinc ion intercalation, which often led to structural collapse, loss of water of crystallization and capacity decay, limiting the performance of MoS2 in practical applications. Summary of the Invention

[0006] To address the shortcomings of existing technologies, the present invention aims to provide a method and application for controlling the interlayer spacing of molybdenum disulfide by oxygen doping. This method utilizes an oxygen doping strategy to prepare molybdenum disulfide with extended interlayer spacing (O-MoS2@CC), which, when applied to aqueous zinc-ion batteries, can significantly improve the insertion / extraction kinetics and structural stability of zinc ions.

[0007] To achieve the above objectives, the present invention adopts the following technical solution: This invention provides a method for controlling the interlayer spacing of molybdenum disulfide by oxygen doping, comprising the following steps: (1) Cut the carbon cloth into pieces and soak them in hydrogen peroxide solution. After oil bath, remove the carbon cloth, wash it, and dry it.

[0008] (2) Dissolve ammonium molybdate tetrahydrate and thiourea in deionized water, stir, and then transfer the mixed solution and the carbon cloth pretreated in step (1) to a high-pressure reactor for hydrothermal reaction. After the reaction is completed, the product is cooled, washed and dried to obtain oxygen-doped molybdenum disulfide grown in situ on the carbon cloth. Introducing oxygen doping into molybdenum disulfide expands the interlayer spacing in molybdenum disulfide.

[0009] Preferably, the mass fraction of hydrogen peroxide solution in step (1) of the present invention is 30%.

[0010] Preferably, the oil bath temperature in step (1) of the present invention is 70 °C and the time is 7 h.

[0011] Preferably, in step (2) of the present invention, the amount of ammonium molybdate tetrahydrate added is 1.00 mmol and the amount of thiourea added is 33.00 mmol.

[0012] Preferably, the hydrothermal reaction temperature in step (2) of the present invention is 180 °C and the time is 24 h; the drying temperature is 60 °C and the time is 12 h; as a further preferred embodiment of the present invention, the O-MoS2@CC material obtained in step (2) is characterized by: determining the crystal structure and phase type of the O-MoS2@CC material by X-ray diffraction (XRD), studying the morphology and microstructure of the material by field emission scanning electron microscopy (SEM), analyzing the internal structure and micromorphology of the material by transmission electron microscopy (TEM), and studying the elemental composition and atomic valence state of the material by X-ray photoelectron spectroscopy (XPS).

[0013] Another objective of this invention is the application of the oxygen-doped molybdenum disulfide material prepared by the method in the preparation of battery cathode materials.

[0014] Preferably, the battery of the present invention is an aqueous zinc-ion battery, specifically including a battery negative electrode shell, a negative electrode, a separator, an electrolyte, an oxygen-doped molybdenum disulfide positive electrode, a gasket, and a battery positive electrode shell.

[0015] The preparation process of the aqueous zinc-ion battery is a conventional process, specifically as follows: the prepared O-MoS2@CC material is cut into round pieces to obtain the positive electrode; zinc foil is polished and cut into round pieces, ultrasonically cleaned, and dried at room temperature to obtain the negative electrode; a glass fiber membrane is used as the separator, and Zn(CF3SO3)2 is used as the electrolyte; then the battery negative electrode shell, negative electrode, separator, electrolyte, positive electrode, gasket, and battery positive electrode shell are assembled into a standard CR2032 coin cell, and activated after standing; the electrochemical performance of the battery is studied through cyclic voltammetry, constant current charge-discharge testing, cycle performance testing, and rate performance testing.

[0016] Compared with the prior art, the present invention has the following beneficial effects: (1) This invention utilizes the incomplete hydrothermal reaction at low temperatures to introduce oxygen doping into molybdenum disulfide, achieving the beneficial effect of effectively expanding the interlayer spacing in molybdenum disulfide. Conventional high-temperature hydrothermal processes cause excessive reaction between molybdate and thiourea, inhibiting oxygen doping and making it difficult to achieve effective interlayer spacing expansion. Low-temperature hydrothermal processes, by controlling the degree of precursor reaction and introducing structural defects and oxygen doping, successfully achieve significant expansion of the interlayer spacing. On the one hand, the bond length of the Mo-O bond is much shorter than that of the Mo-S bond. The S atom vacancy defects generated simultaneously during the oxygen doping process will destroy the originally regular interlayer structure of molybdenum disulfide, effectively weakening the van der Waals forces between adjacent molybdenum disulfide layers, providing a structural basis for widening the interlayer spacing. On the other hand, O 2- Compared to S 2- With a larger charge-to-mass ratio, O doped into the crystal lattice 2- The electrostatic repulsion between them is much stronger than that between S in the original molybdenum disulfide. 2- The electrostatic repulsion between them.

[0017] (2) This invention prepares O-MoS2@CC material with effectively extended interlayer spacing through oxygen doping strategy and applies it to aqueous zinc-ion battery, achieving the beneficial effect of optimizing zinc-ion storage capacity. This preparation method can expand the interlayer spacing of MoS2 from 0.62 nm to 0.90 nm, significantly improving zinc-ion storage capacity and stability, and increasing energy density and cycle stability. System characterization and electrochemical testing show that the material exhibits excellent specific capacity and cycle life. It not only provides an effective new doping regulation approach for the design of high-performance aqueous zinc-ion battery cathode materials, but also has important scientific significance for understanding the zinc-ion storage mechanism in layered materials, and expands the selection range of aqueous zinc-ion battery cathode materials, providing more ideas for the modification of cathode materials, and has reference significance for exploring the complex zinc storage mechanism in MoS2-based aqueous zinc-ion batteries. Attached Figure Description

[0018] Figure 1This is a flowchart of Embodiment 1 of the present invention.

[0019] Figure 2 These are the XRD and XPS spectra of the materials in Example 1 and Comparative Example 1 of the present invention; (a) XRD curves of MoS2@CC and O-MoS2@CC; (b) XPS spectrum of O-MoS2@CC; (c) XPS spectrum of Mo 3d; (d) XPS spectrum of S 2p; (e) XPS spectrum of O 1s.

[0020] Figure 3 These are the SEM, TEM, HRTEM, and EDS spectra of the materials in Example 1 and Comparative Example 1 of the present invention; (a) and (b) SEM images of MoS2@CC; (c) TEM image of MoS2@CC; (d) SEM image of O-MoS2@CC; (e) SEM image of the cross section of O-MoS2@CC; (f) TEM image of O-MoS2@CC; (g) HRTEM image of MoS2@CC; (h) HRTEM image of O-MoS2@CC; and (i) EDS spectrum of O-MoS2@CC.

[0021] Figure 4 These are the performance curves of the batteries in Example 1 and Comparative Example 1 of the present invention; (a) Zn-O-MoS2@CC battery at 0.1 mV S -1 (a) CV curves of the first two cycles at the scan rate; (b) O-MoS2@CC at 0.1 A g -1 Charge-discharge curves at current densities; (c) O-MoS2@CC at 0.1~3 A g -1 Rate performance at various current densities; (d) MoS2@CC at 0.5 A g -1 Cycling performance at current density; (e) O-MoS2@CC at 0.5 A g -1 Cyclic performance at current density.

[0022] Figure 5 These are the cyclic voltammetry (CV) curves of Embodiment 1 of the present invention; (a) CV curves of O-MoS2@CC at different scan rates; (b) and (c) The corresponding linear relationship between peak current and potential curves in logarithmic coordinates; (d) The contribution rates of capacitance and diffusion-limited capacitance at different scan rates. Detailed Implementation

[0023] The technical solutions of the embodiments of the present invention will be clearly and completely described below with reference to the accompanying drawings. Obviously, the described embodiments are only some embodiments of the present invention, and not all embodiments. Based on the embodiments of the present invention, all other embodiments obtained by those skilled in the art without creative effort are within the scope of protection of the present invention.

[0024] Example 1 A method for controlling the interlayer spacing of molybdenum disulfide by oxygen doping and its application are detailed below: (1) Soak the carbon cloth in 30% hydrogen peroxide by mass, and then in an oil bath at 70 °C for 7 h. Remove the soaked carbon cloth, wash it thoroughly with distilled water, and dry it in an oven.

[0025] (2) Add 1.00 mmol of ammonium molybdate tetrahydrate ((NH4)6Mo7O 24 ·4H2O) and 33.00 mmol of thiourea (CS(NH2)2) were dissolved in 40 mL of deionized water to obtain a mixed solution. After magnetic stirring for 30 min, the mixed solution and a pretreated CC were transferred to a 100 mL polytetrafluoroethylene-lined high-pressure reactor and reacted at 180 °C for 24 h. After the reaction, the product was naturally cooled, thoroughly washed with deionized water, and dried at 60 °C to finally obtain O-MoS2@CC material. Samples were taken and the O-MoS2@CC samples were characterized.

[0026] (3) The O-MoS2@CC material was cut into circular pieces with a diameter of 14 cm to make the positive electrode; the zinc foil was polished with 1200-grit sandpaper and cut into circular pieces with a diameter of 16 mm, ultrasonically cleaned with anhydrous ethanol, and naturally dried at room temperature to obtain the negative electrode; the separator was a Whatman glass fiber membrane (16 mm); the electrolyte was a 3 mol / L solution. 1 A Zn(CF3SO3)2 solution was used. The negative electrode shell, negative electrode, separator, electrolyte, positive electrode, gasket, and positive electrode shell of the battery were assembled into a standard CR2032 coin cell in air. The cell was left to stand at room temperature for 6 hours, and then treated with 0.1 A g... -1 The battery was activated by cycling at a low current density for 10 cycles; the electrochemical performance of the battery was studied through cyclic voltammetry, constant current charge-discharge testing, cycle performance testing, and rate performance testing.

[0027] This embodiment characterizes the phase types, crystal structure, elemental composition, and atomic valence states of the O-MoS2@CC material using XRD, and the results are as follows: Figure 2 (a) and Figure 2As shown in (b): the (002) diffraction peak of the O-MoS2@CC cathode material is located at 9.8°, according to the Bragg equation. The interlayer spacing of the O-MoS2@CC cathode material was calculated to be 0.90 nm. The XPS spectrum of the oxygen-doped MoS2 material in this embodiment showed three peaks, attributed to Mo, S, and O, respectively. The XPS values ​​for Mo 3d and S 2p were as follows: Figure 2 As shown in (c) and (d), the high-resolution Mo 3d spectrum of oxygen-doped MoS2 exhibits two peaks at 231.7 eV and 228.8 eV, which are attributed to Mo, respectively. 4+ 3D 3 / 2 and Mo 4+ 3D 5 / 2 Furthermore, a peak at 226.3 eV was observed, attributed to S 2s; in the high-resolution XPS spectrum of S 2p, two characteristic peaks at 163.4 eV and 161.9 eV correspond to S 2s and S 2p, respectively. 2- 2p 1 / 2 and S 2- 2p 3 / 2 ; O 1s XPS such as Figure 2 As shown in (e), the signals at 531.5 eV and 533.2 eV are related to Mo-O bonds and adsorbed water, respectively.

[0028] The SEM characterization results of the O-MoS2@CC material in this embodiment are as follows: Figure 3 As shown in (d), the O-MoS2@CC material in this embodiment has a layered structure, with nanosheets growing vertically and uniformly on the carbon cloth substrate. This effectively inhibits layer stacking and promotes the electrolyte wettability of the positive electrode active material, thereby benefiting Zn. 2+ Rapid migration.

[0029] The TEM characterization results of the O-MoS2@CC material in this embodiment are as follows: Figure 3 As shown in (f), a typical nanosheet structure can be clearly seen; at the same time, from Figure 3 The thickness of the O-MoS2@CC material can be measured to be 348.7 nm in the cross-sectional SEM image of the O-MoS2@CC material shown in (e).

[0030] The EDS characterization results of the O-MoS2@CC material in this embodiment are as follows: Figure 3 As shown in (i), the uniform distribution of Mo, S and O elements in the prepared nanosheet O-MoS2@CC material can be clearly seen, which indicates the successful synthesis of the material and its potential for further electrochemical testing.

[0031] This study employed HRTEM testing to deeply analyze the internal microstructure of the material and quantify the interlayer spacing changes of MoS2 after oxygen doping treatment. The test results are as follows: Figure 3 As shown in (h), the interlayer spacing of the O-MoS2@CC material in this embodiment is 0.90 nm, which is consistent with the calculation result.

[0032] The results of the electrochemical performance test in this embodiment are as follows: Figure 4 As shown: To further explore the insertion and extraction mechanism of zinc ions in O-MoS2@CC zinc-ion batteries, cyclic voltammetry (CV) was used to study the material. Figure 4 (a) The Zn-O-MoS2@CC cell at 0.1 mV S is given. -1 The CV curves for the first two rotations at a scan rate of 0.67 / 1.13V; Zn 2+ A redox peak appeared at / Zn, corresponding to Zn 2+ The embedding and extraction behavior of Zn; with increasing cycle number, the area enclosed by the CV curve expands; indicating that during the initial activation process of the material, Zn... 2+ Intercalation increases the interlayer spacing, providing more storage space for the intercalation of more ions, thereby improving the reversibility of the cathode material.

[0033] To evaluate the cycling stability of the O-MoS2@CC electrode, constant current charge-discharge tests were performed. Figure 4 (b) O-MoS2@CC electrode at 0.1 A g -1 The charge-discharge curves at current density show that the charge-discharge plateaus are located at 1.13 V and 0.67 V, respectively, which is consistent with the CV results. Figure 4 (c) Demonstrates the O-MoS2@CC electrode in the range of 0.1~3 A g. -1 Rate performance of O-MoS2@CC electrode at various current densities at 3 A g -1 The zinc storage capacity at the specified current density is 122.1 mAh g. -1 In addition, when the multiplier is adjusted to 0.1 Ag -1 The specific capacity can quickly recover to 220.5mAh g. -1 This indicates that the O-MoS2@CC electrode has excellent rate performance.

[0034] Meanwhile, the O-MoS2@CC electrode exhibits excellent cycling stability, from Figure 4 As shown in (e), the initial capacity of the O-MoS2@CC electrode is 198.5 mAh g. -1 After 3000 cycles, the capacity retention rate is approximately 96.3%, and the coulomb efficiency is relatively stable.

[0035] To elucidate the excellent zinc ion storage performance of the material, cyclic voltammetry was used to investigate its electrochemical reaction characteristics. The results are as follows: Figure 5 As shown; generally, peak current ( ) and scan rate ( )related: Where a and b are variable parameters, and the value of b is determined by... and The slope is obtained; such as Figure 5 (c) The b-values ​​for the oxidation and reduction peaks are 0.85 and 0.83, respectively; the kinetic control of the electrochemical reaction in the MoS2 electrode has two types: capacitance contribution. and ion diffusion contribution ,formula: ,like Figure 5 (d), scan rate from 0.1 mV / s -1 up to 1.0 mVs -1 The capacitance contribution to the total capacity ranges from 62% to 88%. A higher capacitance contribution rate means that during battery charging and discharging, the electrode surface or near the surface can more effectively attract and fix ions in the electrolyte. This process has faster kinetic characteristics compared to the traditional bulk diffusion mechanism. Since capacitive storage relies on the rapid adsorption and desorption of ions on the electrode surface rather than the slow diffusion inside the solid material, the higher the capacitance contribution rate, the faster the ion storage and release rate, thus significantly improving rate performance. At high current densities, the battery can still maintain high capacity and stable voltage response, meeting the needs of high-power applications.

[0036] Comparative Example 1 The difference between this comparative example and Example 1 lies in the hydrothermal reaction temperature, in order to verify that low temperature is the core condition for oxygen doping, as detailed below: (1) Soak the carbon cloth in 30% hydrogen peroxide by mass, and then in an oil bath at 70 °C for 7 h. Remove the soaked carbon cloth, wash it thoroughly with distilled water, and dry it in an oven.

[0037] (2) Add 1.00 mmol of ammonium molybdate tetrahydrate ((NH4)6Mo7O 24 ·4H2O) and 33.00 mmol of thiourea (CS(NH2)2) were dissolved in 40 mL of deionized water. After magnetic stirring for 30 min, the mixed solution and a pretreated CC were transferred to a 100 mL polytetrafluoroethylene-lined high-pressure reactor and reacted at 220 °C for 24 h. After the reaction, the product was naturally cooled, thoroughly washed with deionized water, and dried at 60 °C to finally obtain MoS2@CC material. Samples were taken and the MoS2@CC samples were characterized.

[0038] (3) The MoS2@CC material was cut into circular pieces with a diameter of 14 cm to make the positive electrode; the zinc foil was polished with 1200-grit sandpaper and cut into circular pieces with a diameter of 16 mm, cleaned with anhydrous ethanol by ultrasonication, and dried naturally at room temperature to obtain the negative electrode; the separator was a Whatman glass fiber membrane (16 mm); the electrolyte was a 3 mol / L solution. 1 A Zn(CF3SO3)2 solution was used. The negative electrode shell, negative electrode, separator, electrolyte, positive electrode, gasket, and positive electrode shell of the battery were assembled into a standard CR2032 coin cell in air. The cell was left to stand at room temperature for 6 hours, and then treated with 0.1 A g... -1 The battery was activated by cycling at a low current density for 10 cycles. The electrochemical performance of the battery was investigated through cyclic voltammetry, constant current charge-discharge testing, cycle performance testing, and rate performance testing.

[0039] This comparative example characterizes the MoS2@CC material by XRD, and the results are as follows: Figure 2 As shown in (a), the (002) diffraction peak of the MoS2@CC material in this comparative example corresponds to 9.8°, according to the Bragg equation. The interlayer spacing of the MoS2@CC material was calculated to be 0.62 nm.

[0040] The MoS2@CC material in this comparative example was characterized and analyzed. Figure 3 Figures (a), (b), and (c) show the morphological characteristics of the MoS2@CC material. As can be seen from the figures, the (002) diffraction peak of the MoS2@CC material in this comparative example corresponds to 9.8°. According to Bragg's equation... The interlayer spacing of the MoS2@CC material was calculated to be 0.62 nm. Due to the excessive loading, MoS2 agglomerated on the carbon cloth, forming a flower-like structure, which is detrimental to Zn growth. 2+ Rapid migration reduces migration rate.

[0041] HRTEM testing was used to analyze the internal microstructure of the comparative MoS2@CC material, quantifying the variation in MoS2 interlayer spacing. The test results are as follows: Figure 3 As shown in (g), the interlayer spacing of the MoS2@CC sample is 0.62 nm, which is consistent with the calculated result.

[0042] The electrochemical performance test results in this comparative example are as follows: Figure 4 (d) shows that the initial capacity of the MoS2@CC cathode material in this comparative example is 162.8 mAh g. -1 After 2500 cycles, the capacity retention rate is about 85%, and the coulomb efficiency is low.

[0043] Table 1 shows a comparison of the test results of Example 1 and Comparative Example 1.

[0044] Table 1 Comparison of test results between Example 1 and Comparative Example 1 In Comparative Example 1 and Example 1 of this invention, MoS2@CC and O-MoS2@CC were successfully prepared by hydrothermal method, respectively. The characteristic peaks of the XRD curve of the synthesized MoS2@CC were consistent with those of the standard card JCPDS No. 75-1593, indicating that the material was successfully synthesized. Moreover, the shapes of the two characteristic peaks did not change significantly, indicating that the structure was not damaged.

[0045] As shown in Table 1, the interlayer spacing of the O-MoS2@CC cathode material prepared in Example 1 of this invention is 0.90 nm, and the initial capacity is 198.5 mAh g. -1 After 3000 cycles, the capacity retention was approximately 96.3%, and the coulombic efficiency was relatively stable. The interlayer spacing of the MoS2@CC cathode material prepared in Comparative Example 1 was 0.62 nm, and the initial capacity was 162.8 mAh g⁻¹. -1 After 2500 cycles, the capacity retention rate is about 85%, and the coulomb efficiency is low.

[0046] In Example 1, the O-MoS2@CC cathode material exhibits a large interlayer spacing, indicating that successful oxygen doping at low temperatures can effectively expand the interlayer spacing of MoS2, which is beneficial for the rapid insertion and extraction of zinc ions, verifying the effective control of the MoS2 crystal structure by oxygen doping. The O-MoS2@CC electrode in Example 1 also demonstrates excellent cycle stability, indicating that oxygen doping increases the interlayer spacing of MoS2, significantly improving the specific capacity and cycle stability of the MoS2@CC electrode. This is due to the shorter Mo-O bonds and S atom vacancies, which effectively weaken the van der Waals forces between adjacent MoS2 layers. Considering the O... 2- Compared to S ions 2- The ions have a larger charge-to-mass ratio, suggesting that O in the layered structure of MoS2 is more likely to be present. 2- The electrostatic repulsion between them is stronger than that between S 2- Oxygen doping significantly increases the interlayer spacing; furthermore, oxygen doping causes lattice distortion in MoS2, generating numerous defects that provide fertile ground for Zn. 2+ The storage provides more active sites.

[0047] Although embodiments of the invention have been shown and described, it will be understood by those skilled in the art that various changes, modifications, substitutions and alterations can be made to these embodiments without departing from the principles and spirit of the invention, the scope of which is defined by the appended claims and their equivalents.

Claims

1. A method for controlling the interlayer spacing of molybdenum disulfide layers by oxygen doping, characterized in that, Includes the following steps: (1) Cut the carbon cloth into pieces and soak them in hydrogen peroxide solution. After oil bath, remove the carbon cloth, wash it, and dry it. (2) Dissolve ammonium molybdate tetrahydrate and thiourea in deionized water, stir, and then transfer the mixed solution and the carbon cloth pretreated in step (1) to a high-pressure reactor for hydrothermal reaction. After the reaction is completed, the product is cooled, washed and dried to obtain oxygen-doped molybdenum disulfide grown in situ on the carbon cloth. Introducing oxygen doping into molybdenum disulfide expands the interlayer spacing in molybdenum disulfide.

2. The method for controlling the interlayer spacing of molybdenum disulfide layers by oxygen doping according to claim 1, characterized in that, The mass fraction of hydrogen peroxide solution in step (1) is 30%.

3. The method for controlling the interlayer spacing of molybdenum disulfide layers by oxygen doping according to claim 1, characterized in that, The oil bath temperature in step (1) is 70 °C and the time is 7 h.

4. The method for controlling the interlayer spacing of molybdenum disulfide layers by oxygen doping according to claim 1, characterized in that, The amount of ammonium molybdate tetrahydrate added in the mixed solution of step (2) is 1.00 mmol, and the amount of thiourea added is 33.00 mmol.

5. The method for controlling the interlayer spacing of molybdenum disulfide layers by oxygen doping according to claim 1, characterized in that, The hydrothermal reaction temperature in step (2) is 180 ℃ and the time is 24 h; the drying temperature is 60 ℃ and the time is 12 h.

6. The application of the oxygen-doped molybdenum disulfide material prepared by the method according to any one of claims 1 to 5 in the preparation of battery cathode materials.

7. The application according to claim 6, characterized in that: The battery is an aqueous zinc-ion battery, specifically comprising a battery negative electrode shell, a negative electrode, a separator, an electrolyte, an oxygen-doped molybdenum disulfide positive electrode, a gasket, and a battery positive electrode shell.

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