Lithium-rich manganese-based material with spinel@Na2SeO3 structure and preparation method

Abstract

The present invention relates to the technical field of lithium-ion batteries, and more specifically, to a lithium-rich manganese-based material with a spinel@Na2SeO3 structure and a preparation method thereof. The method comprises mixing and grinding a lithium-rich manganese-based positive electrode material with sodium selenite, and calcining the mixture under an argon atmosphere to obtain a lithium-rich manganese-based material with a spinel@Na2SeO3 structure. The method can make the surface Se 4+ A reduction reaction occurs, initiating the formation of Mn on the surface of the material. 4+ Reduced to Mn 3+ , Mn 3+ A spinel structure is formed on the surface of the material; the Na2SeO3 coating can produce abundant oxygen vacancies on the surface of the material, effectively inhibiting the release of unstable oxygen during the cycle and protecting the active material from corrosion by the electrolyte; as an in-situ spinel phase, it can provide a three-dimensional lithium ion transmission channel, thereby effectively accelerating the transmission of lithium ions and making the electrochemical performance of the material better.

Description

Technical Field

[0001] The present invention relates to the technical field of lithium-ion batteries, and more particularly, to a lithium-rich manganese-based material having a spinel@Na2SeO3 structure and a preparation method thereof. Background Art

[0002] With the rapid development of electric vehicles and energy storage devices, electrochemical energy storage batteries with high energy density and low cost, such as lithium-ion batteries (LIBs), have attracted increasing attention. Lithium-rich manganese-based materials (xLi2MnO3·(1-x)LiTMO2, 0 < x < 1, TM = Mn, Co, Ni, etc.) are considered to be one of the most promising cathode materials due to their specific capacity exceeding 250 mAhg -1 . Generally, the high specific capacity of lithium-rich manganese-based oxide materials not only comes from the redox reaction of transition metal ions in the low voltage range, but may also come from the redox reaction of oxygen anions at high voltages. Irreversible oxygen evolution inevitably brings certain structural distortion and irreversible capacity loss, resulting in extremely low ICE and electrochemical performance.

[0003] Since the removal of unstable oxygen always occurs at the electrode / electrolyte interface and is accompanied by various side reactions, surface coating has become one of the most effective ways to improve the electrochemical performance of electrode materials. The coated surface can serve as a protective layer for the active material, reducing irreversible capacity loss. At the same time, the presence of oxygen vacancies and spinel phases on the surface helps to inhibit irreversible oxygen release and enhance lithium ion diffusion.

[0004] In the field of lithium-ion batteries, there are many substances that can be used for surface coating. The coating material should have the advantages of high Li + mobility and good structural stability. Generally, metal oxides, fluorides, metal phosphates, carbon materials, and polymer conductive materials are used as surface coating materials to improve the electrochemical performance of lithium-rich materials. However, the most fundamental problems, namely the irreversible loss of lattice oxygen and the side reactions between the electrode / electrolyte interface, have not been solved. Uniform Se 6+ doping can improve the crystallinity of Li2MnO3, thereby making the atomic arrangement in the transition metal layer of the lithium-rich manganese-based cathode material more orderly. Unfortunately, this modification method has not significantly improved the electrochemical performance. Summary of the Invention

[0005] The technical problem to be solved by the present invention is to provide a lithium-rich manganese-based material having a spinel@Na2SeO3 structure and a preparation method thereof to solve the problem of poor electrochemical performance of the cathode material in the prior art.

[0006] The technical solution of the present invention to solve the above technical problems is as follows:

[0007] The present invention provides a method for preparing a lithium-rich manganese-based material having a spinel@Na2SeO3 structure. The lithium-rich manganese-based positive electrode material is mixed with sodium selenite and ground, and then calcined under an argon environment to obtain the lithium-rich manganese-based material having the spinel@Na2SeO3 structure.

[0008] On the basis of the above technical solution, the present invention can also be improved as follows.

[0009] Furthermore, the calcination temperature is 330° C. to 370° C., and the calcination time is 2 to 4 hours.

[0010] Furthermore, based on the total mass after mixing being 100%, the mass percentage of the sodium selenite is 1 wt% to 4 wt%.

[0011] Furthermore, the lithium-rich manganese-based positive electrode material is Li 1.2 Mn 0.54 Ni 0.13 Co 0.13 O2 material.

[0012] Furthermore, the Li 1.2 Mn 0.54 Ni 0.13 Co 0.13 The preparation method of O2 material is co-precipitation-high temperature solid phase method.

[0013] Furthermore, the coprecipitation-high temperature solid phase method comprises the following steps:

[0014] S1, prepare the mixture containing Mn 2+ 、Ni 2+ 、Co 2+ A mixed sulfate solution, a Na2CO3 solution and an ammonium bicarbonate aqueous solution; wherein the Mn 2+ 、Ni 2+ 、Co 2+ The molar ratio is 54:13:13, the total cation concentration is 2 mol / L, the concentration of the Na2CO3 solution is 2 mol / L, and the concentration of the ammonium bicarbonate aqueous solution is 0.12 mol / L;

[0015] S2. Simultaneously injecting the mixed sulfate solution and the Na2CO3 solution into the preheated aqueous ammonium bicarbonate solution, stirring and reacting, and after the reaction is completed, standing and aging to obtain a product; the feed rate of the mixed sulfate solution and the Na2CO3 solution is 0.5 mL / min; and the reaction time is 15 to 17 h;

[0016] S3, filtering, separating, washing, and drying the product in sequence to obtain a carbonate precursor powder;

[0017] S4, mixing and grinding the precursor powder with lithium carbonate, wherein the molar ratio of the precursor powder to the lithium carbonate is 1:1.35; then pre-calcining and high-temperature calcining are performed in sequence to obtain the Li 1.2 Mn 0.54 Ni 0.13 Co 0.13 O2 material; the pre-firing temperature is 550 ℃ ~ 650 ℃, the time is 4 to 6 hours, the high temperature calcination temperature is 850 ~ 950 ℃, the time is 10 to 12 hours.

[0018] Furthermore, in step S2, the preheating temperature is 53°C to 57°C.

[0019] Furthermore, in step S2, the temperature of the static aging is 55° C. and the time is 12 hours.

[0020] The present invention also provides a lithium-rich manganese-based material having a spinel@Na2SeO3 structure, which is prepared by the above method.

[0021] The present invention also provides a lithium-ion battery prepared using the lithium-rich manganese-based material as described above.

[0022] The beneficial effects of the present invention are:

[0023] (1) The preparation method of the lithium-rich manganese-based material with a spinel @ Na2SeO3 structure of the present invention comprises mixing sodium selenite with a lithium-rich manganese-based positive electrode material and calcining the mixture to make the Se on the surface of Na2SeO3 4+ A reduction reaction occurs, initiating the formation of Mn on the surface of the material. 4+ Reduced to Mn 3+ , Mn 3+ The appearance of induced the formation of a spinel structure on the surface of the material, and finally a lithium-rich manganese-based material with a spinel@Na2SeO3 structure was obtained;

[0024] (2) The preparation method of the lithium-rich manganese-based material having a spinel@Na2SeO3 structure of the present invention, the Na2SeO3 coating layer can generate abundant oxygen vacancies on the surface of the material, effectively inhibiting the release of unstable oxygen during the cycle and protecting the active material from corrosion by the electrolyte; as an in-situ spinel phase, it can provide a three-dimensional lithium ion transmission channel, thereby effectively accelerating the transmission of lithium ions;

[0025] (3) The preparation method of the lithium-rich manganese-based material having a spinel@Na2SeO3 structure of the present invention has simple steps, mild reaction conditions and low preparation cost;

[0026] (4) The lithium-rich manganese-based material having a spinel@Na2SeO3 structure of the present invention, Na2SeO3 coating can enhance the structural stability of the material surface, thereby reducing structural rearrangement during charge and discharge;

[0027] (5) The lithium-rich manganese-based material with a spinel@Na2SeO3 structure of the present invention has better electrochemical properties, and its discharge specific capacity and initial coulombic efficiency are effectively improved; the capacity retention rate after 200 cycles at 0.5C and 1C rates, the specific capacity at 10C rate, and the voltage drop after 200 cycles are all improved to varying degrees. BRIEF DESCRIPTION OF THE DRAWINGS

[0028] Figure 1 The preparation method of the lithium-rich manganese-based material with a spinel@Na2SeO3 structure of the present invention, the lattice structure analysis diagram of Example 2, Figure 1 a is the XRD pattern of each sample, Figure 1 b in the middle is the Raman spectrum of each sample;

[0029] Figure 2 The preparation method of the lithium-rich manganese-based material with a spinel@Na2SeO3 structure of the present invention, the microscopic morphology analysis diagram of Example 3, Figure 2 a and b are SEM images of NSO-0. Figure 2 c and d are SEM images of NSO-1%, Figure 2 Figures e and f are SEM images of NSO-2%. Figure 2 Figures g and h are SEM images of NSO-3%. Figure 2 The i and j are SEM images of NSO-4%. Figure 2 k is the EDS mapping diagram of NSO-3%, Figure 2 Mn, Ni, Co, and Se are element distribution diagrams of element Mn, element Ni, element Co, and element Se respectively;

[0030] Figure 3 The preparation method of the lithium-rich manganese-based material having a spinel@Na2SeO3 structure of the present invention, and the microstructure diagram of Example 3; Figure 3 a is the HR-TEM image of NSO-0. Figure 3 b is the FFT image of NSO-0. Figure 3 The c image is the HR-TEM image of NSO-3%. Figure 3 (d) is the FFT image of NSO-3%;

[0031] Figure 4 The preparation method of the lithium-rich manganese-based material having a spinel@Na2SeO3 structure of the present invention, the XPS graph of each sample in Example 3; Figure 4a in the figure is the Mn 2p spectrum, Figure 4 b in the figure is Ni 2p spectrum, Figure 4 c in the figure is the Co 2p spectrum, Figure 4 In the figure, d is the O1s spectrum. Figure 4 The middle e is the full spectrum, Figure 4 f in the middle is Se 3d spectrum;

[0032] Figure 5 This is a preparation method of a lithium-rich manganese-based material having a spinel@Na2SeO3 structure according to the present invention, and an electrochemical performance analysis diagram of Example 4; Figure 5 a is the initial charge and discharge curve, Figure 5 b is the first cycle cyclic voltammetry curve at 0.1mV / s. Figure 5 In the figure c is the rate performance diagram at 0.1-10C. Figure 5 d in the middle is the average voltage decay curve under 1C, Figure 5 e in the middle is the cycle curve at 0.5C, Figure 5 The middle f is the cycle curve under 1C;

[0033] Figure 6 This is a kinetic test diagram of Example 5 of the preparation method of the lithium-rich manganese-based material having a spinel@Na2SeO3 structure of the present invention; Figure 6 a in the middle is the EIS graph of each sample, Figure 6 b is Z under low-frequency electrochemical impedance spectroscopy w and ω -1 / 2 The relationship diagram between . DETAILED DESCRIPTION

[0034] The principles and features of the present invention are described below with reference to the accompanying drawings. The examples given are only used to explain the present invention and are not used to limit the scope of the present invention.

[0035] The preparation method of the lithium-rich manganese-based material having a spinel@Na2SeO3 structure of the present invention comprises mixing and grinding a lithium-rich manganese-based positive electrode material with sodium selenite, and calcining the mixture under an argon environment to obtain a lithium-rich manganese-based material having a spinel@Na2SeO3 structure.

[0036] The preparation method of the lithium-rich manganese-based material with a spinel @ Na2SeO3 structure of the present invention comprises mixing sodium selenite with a lithium-rich manganese-based positive electrode material and calcining the mixture to make the Se on the surface of Na2SeO3 4+ A reduction reaction occurs, initiating the formation of Mn on the surface of the material. 4+ Reduced to Mn 3+ , Mn 3+The presence of Na2SeO3 induces the formation of a spinel structure on the surface of the material, ultimately resulting in a lithium-rich manganese-based material with a spinel@Na2SeO3 structure. The Na2SeO3 coating enhances the structural stability of the material surface, thereby reducing structural rearrangements during charge and discharge.

[0037] The preparation method of the present invention has the advantages of simple steps, mild reaction conditions, low preparation cost and good coating effect.

[0038] The preparation method of the present invention can obtain Li with an in-situ spinel phase and a Na2SeO3 coating layer. 1.2 Mn 0.54 Ni 0.13 Co 0.13 O2 material. The Na2SeO3 coating can generate abundant oxygen vacancies on the material surface, effectively suppressing unstable oxygen release during cycling and protecting the active material from electrolyte corrosion. As an in-situ spinel phase, it can provide three-dimensional lithium ion transport channels, thereby effectively accelerating the transport of lithium ions.

[0039] Preferably, in the preparation method of the present invention, the calcination temperature is 330° C. to 370° C., and the calcination time is 2 to 4 hours.

[0040] More preferably, the calcination temperature is 350° C. and the calcination time is 3 h.

[0041] Preferably, based on the total mass after mixing being 100 wt %, the mass percentage of sodium selenite is 1 wt % to 4 wt %.

[0042] Further preferably, the mass percentage of sodium selenite is 3 wt %.

[0043] More preferably, the lithium-rich manganese-based positive electrode material is Li 1.2 Mn 0.54 Ni 0.13 Co 0.13 O2 material (LMR material).

[0044] Li of the present invention 1.2 Mn 0.54 Ni 0.13 Co 0.13 The preparation method of O2 material is a co-precipitation-high temperature solid phase method, which includes the following steps:

[0045] S1, prepare the mixture containing Mn 2+ 、Ni 2+ 、Co 2+ A mixed sulfate solution, a Na2CO3 solution and an ammonium bicarbonate aqueous solution; wherein the Mn in the mixed sulfate solution 2+ 、Ni 2+ 、Co2+ The molar ratio is 54:13:13, the total cation concentration is 2 mol / L, the concentration of Na2CO3 solution is 2 mol / L, and the concentration of ammonium bicarbonate aqueous solution is 0.12 mol / L.

[0046] S2. Simultaneously inject the mixed sulfate solution and the Na2CO3 solution into the preheated aqueous ammonium bicarbonate solution, stir and react, and after the reaction is completed, let it stand and age to obtain a product; the feed rate of the mixed sulfate solution and the Na2CO3 solution is 0.5 mL / min.

[0047] Preferably, the stirring rate is 800-1200 rpm / min, the pH value of the reaction solution is 8, and the reaction time is 15-17 h.

[0048] Preferably, the preheating temperature is 53°C to 57°C.

[0049] Preferably, the temperature for static aging is 55° C. and the time is 12 h.

[0050] S3. The product is filtered, separated, washed and dried in sequence to obtain carbonate precursor powder.

[0051] S4, mixing and grinding the precursor powder with lithium carbonate, wherein the molar ratio of the precursor powder to the lithium carbonate is 1:1.35; then pre-calcining and high-temperature calcining are performed in sequence to obtain Li 1.2 Mn 0.54 Ni 0.13 Co 0.13 O2 material; the pre-firing temperature is 550℃~650℃, the time is 4~6h, and the high-temperature calcination temperature is 850~950℃, the time is 10~12h.

[0052] The lithium-rich manganese-based material having a spinel@Na2SeO3 structure of the present invention is prepared by the above-mentioned method.

[0053] The lithium-rich manganese-based material of the present invention can improve the electrochemical performance of the LRM positive electrode material after being coated with Na2SeO3. This is attributed to the synergistic effect produced by the stability of the reduction-induced electrochemically active spinel intermediate layer and the coating layer on the surface of the material. The stability of the surface structure of the material is improved after coating modification.

[0054] Preferably, the LMR material modified with 3 wt% Na2SeO3 exhibits better electrochemical performance, with a discharge capacity and initial coulombic efficiency of up to 285.5 mAhg -1 and 84.6%; the capacity retention rates after 200 cycles at 0.5C and 1C rates are 86.4% and 68.5% respectively; the specific capacity at 10C rate is 87.4 mAh g -1; After 200 cycles, the voltage drop is 0.4445V.

[0055] The present invention is described below by means of specific examples.

[0056] Example 1 Preparation of lithium-rich manganese-based materials with different Na2SeO3 coating amounts

[0057] This embodiment adopts the method of the present invention to prepare a lithium-rich manganese-based material having a spinel@Na2SeO3 structure. The specific preparation process is as follows:

[0058] Li was prepared by co-precipitation combined with high-temperature solid-phase method 1.2 Mn 0.54 Ni 0.13 Co 0.13 O2 material.

[0059] First, according to Mn 2+ :Ni 2+ :Co 2+ 4.5 g MnSO4, 1.86 g CoSO4 and 1.73 g NiSO4 were weighed in a molar ratio of 54:13:13, added to 20 mL deionized water, and ultrasonically dissolved to obtain a mixed sulfate solution with a total cation concentration of 2 mol / L; 4.25 g Na2CO3 was weighed and added to 20 mL deionized water to obtain a 2 mol / L Na2CO3 solution; 20 mL of 0.12 mol / L ammonium bicarbonate aqueous solution was prepared, injected into a round-bottom flask, and heated to 55°C in an oil bath for use.

[0060] Next, a syringe pump was used to simultaneously inject the mixed sulfate solution and Na2CO3 solution into the preheated ammonium bicarbonate solution at a feed rate of 0.5 mL / min. During the reaction, the solution was stirred at 1000 rpm / min and maintained at a pH of 8 to ensure consistent nucleation and growth rates. After the addition of the feeds, the reaction was continued for 16 hours. After completion, the reaction was allowed to age at 55°C for 12 hours.

[0061] Subsequently, the aged sample was filtered and separated, and washed with a large amount of deionized water and ethanol solution (to remove Na + NH 4 + and SO4 2- The cleaned sample was placed in a vacuum drying oven for drying at 80°C for 24h to obtain a light pink carbonate precursor powder.

[0062] Finally, the precursor powder was mixed and ground with lithium carbonate (the molar ratio of precursor to lithium carbonate was 1:1.35). The mixed sample was pre-sintered at 600°C for 5 hours in a tube furnace and then calcined at 900°C for 12 hours to obtain a lithium-rich manganese-based positive electrode material, which was labeled LRM.

[0063] Sodium selenite (Na2SeO3) and LRM powders with mass fractions of 1wt%, 2wt%, 3wt% and 4wt% were ground in a mortar for 1h, and the obtained solid mixtures were calcined at 350℃ for 3h under argon atmosphere. 4+ A reduction reaction occurs, causing Mn 4+ Reduced to Mn 3+ .Mn 3+ The appearance of induced the formation of a spinel structure on the surface of the material, and finally a lithium-rich manganese-based material with a spinel@Na2SeO3 structure was obtained.

[0064] According to different coating amounts of Na2SeO3, the materials prepared in this example are marked as NSO-1%, NSO-2%, NSO-3% and NSO-4%, respectively.

[0065] Example 2 Lattice structure analysis of lithium-rich manganese-based materials with different Na2SeO3 coating amounts

[0066] In this example, XRD was used to test the lattice structures of the NSO-1%, NSO-2%, NSO-3% and NSO-4% samples prepared in Example 1. At the same time, for better comparison, LRM without Na2SeO3 coating was also tested, which was recorded as NSO-0. The results are shown in Figure 2. Figure 1 As shown in a.

[0067] according to Figure 1 As can be seen in a, the five samples all have similar diffraction peaks, which can be corresponded to the layered α-NaFeO2 component of the LiMO2 phase with R-3m symmetry. In addition, the weak peak between 20-23° belongs to the superlattice ordering peak of LiMn6 in the transition metal layer Li2MnO3 (C2 / m). In addition, a weak shoulder peak was found around the (101) peak of the NSO-3% and NSO-4% materials, indicating the presence of spinel phase in the two materials. The formation of the spinel phase is attributed to the reduction reaction of Na2SeO3 in an argon atmosphere at 350°C, which triggers the Mn 4+ Reduced to Mn 3+ , thus causing the rearrangement of the surface structure, which can be verified by XPS analysis. It is worth noting that due to the small amount of Na2SeO3 coating, no characteristic peaks corresponding to Na2SeO3 were found.

[0068] Raman spectroscopy is a sensitive method to distinguish between layered and spinel structures, such as Figure 1 The Raman spectra of NSO-0 and NSO-3% samples are shown in b, at 478 cm -1 and 590cm -1 The two main peaks at correspond to the E of the R-3m layered structure. g and A 1g Vibration mode. 430cm -1 A weak broad peak at the Li2MnO3 phase represents the g Vibration model (C2 / m). In addition, compared with NSO-0, NSO-3% has a -1 There is a weak shoulder peak at the center, which is attributed to the Mn-O vibration of the MnO6 octahedron in the spinel structure (Fd-3m). This further confirms the existence of the spinel phase after Na2SeO3 surface modification.

[0069] Example 3 Micromorphology Analysis of Lithium-Rich Manganese-Based Materials with Different Na2SeO3 Coating Amounts

[0070] In this example, the micromorphologies of the NSO-1%, NSO-2%, NSO-3% and NSO-4% samples prepared in Example 1 were analyzed. At the same time, for better comparison, an LRM without Na2SeO3 coating, denoted as NSO-0, was also compared.

[0071] Figure 2 In the figure, aj are SEM images of NSO-0, NSO-1%, NSO-2%, NSO-3% and NSO-4% samples respectively; all five samples are composed of secondary microspheres (5-6 μm) formed by primary nanoparticles (200-300 nm), indicating that the coating layer does not affect the morphology and size of the LRM material. Moreover, as the coating amount increases, the Na2SeO3 coating layer on the surface of the material gradually becomes denser. In addition, EDS was used to detect the presence of the Na2SeO3 coating layer, and the corresponding element distribution diagram is shown in the figure. Figure 2 The element distribution of K, Mn, Ni, Co and Se is shown in the figure. The uniform distribution of Se element indicates that the Na2SeO3 coating layer has been successfully coated on the surface of LRM particles.

[0072] In order to further study the microstructure of LRM materials, two representative materials, NSO-0 and NSO-3%, were tested by TEM. The test results are shown in Figure 2. Figure 3 shown.

[0073] according to Figure 3 As can be seen in Figure a, NSO-0 exhibits clear lattice fringes with a spacing of 0.472 nm, corresponding to the (003) plane of the layered structure. Figure 3As can be seen in Figure b, there are obvious lattice fringes inside NSO-3%, with a spacing of 0.472nm. The lattice spacing in the middle transition zone is 0.237nm, which is related to the (222) crystal plane of the spinel-like structure. In addition, the outer layer is covered with an amorphous layer with a thickness of about 2-3nm. In order to determine the element distribution of the amorphous layer, as mentioned above Figure 2 EDS analysis was performed on the material. In addition to Ni, Co, and Mn, Se was also confirmed to be uniformly distributed on the surface, indicating that the capping layer is likely amorphous Na2SeO3. Based on these test results, a LRM layered@spinel@Na2SeO3 structure was successfully obtained through a facile coating strategy.

[0074] Furthermore, this example uses XPS testing to explore the surface chemical states of NSO-0, NSO-1%, NSO-2%, NSO-3% and NSO-4%. Figure 4 As shown. Figure 4 In a, the peaks at 641.9 eV and 642.8 eV in NSO-0 correspond to the Mn 2p3 / 2 3+ and Mn 4+ After coating modification, NSO-3% Mn 3+ / Mn 4+ The content ratio of NSO-0 is larger than that of NSO-0, indicating that the Mn 4+ Reduced to Mn 3+ , which is related to the formation of spinel phase. Figure 4 As shown in b, the Ni 2p spectra of the two samples can be divided into two peaks at 854.91 and 856.26 eV, corresponding to Ni 2+ and Ni 3+ After Na2SeO3 coating, the peak position of Ni 2p spectrum did not change significantly, indicating that the valence state of Ni was stable. Figure 4 As shown in Figure c, the 2p3 / 2 peak of Co in NSO-0 is at 780.06eV, and the 2p1 / 2 peak is at 795.54eV, indicating that the oxidation state of Co is +3, and the valence state of Co in NSO-3% has not changed significantly. Figure 4 As shown in the O1s spectrum in d, the surface modification process of NaSeO3 can produce more oxygen vacancies in the LMR material. The O1s spectrum shows two obvious characteristic peaks near 529.3eV and 530.8eV, corresponding to lattice oxygen (OMO) and oxygen vacancies, respectively. From the fitting results of the XPS spectrum, it can be seen that due to the formation of the spinel phase, the proportion of oxygen vacancies in the NSO-3% sample is higher than that in the NSO-0 sample. In addition, as Figure 4As shown in Figure 5, in the Se 3d XPS spectrum of the NSO-3% sample, there is a clear peak related to the Se element at 53.7 eV. Combined with other analysis results, it can be further proved that Na2SeO3 was successfully introduced into NSO-3%.

[0075] Example 4 Analysis of electrochemical properties of lithium-rich manganese-based materials with different Na2SeO3 coating amounts

[0076] The electrochemical behavior of LRM materials during the initial cycle is highly dependent on the redox activity of oxygen anions, which plays a crucial role in the subsequent cycling performance of the material. Therefore, during the initial cycle at 0.1C, the typical charge-discharge curves of NSO-0, NSO-1%, NSO-2%, NSO-3% and NSO-4% samples are as follows: Figure 5 As shown in a.

[0077] according to Figure 5 It can be seen that during charging, the slope below 4.5 V is attributed to the Li + The removal of Ni from the LiMO2 component is also accompanied by 2+ / Ni 3+ / Ni 4+ and Co 3+ / Co 4+ The long platform above 4.5V is related to the activation process of Li2MnO3 components, which also involves the oxidation of lattice oxygen and the irreversible loss of oxygen. In the discharge curve, it is worth noting that all the Na2SeO3-modified LRMs with different coating amounts have a platform below 3V, which is attributed to the Li + inserted into the spinel phase, which indicates that the Na2SeO3 surface engineering induced the generation of the spinel phase.

[0078] In addition, the first discharge capacity of the unmodified sample is 240.7 mAh g at a rate of 0.1 C. -1 , ICE is 73.7%. In comparison, the first discharge specific capacities of NSO-1%, NSO-2%, and NSO-3% are 249.9, 259.7, and 285.5 mAh g, respectively. -1 The improved ICEs were 73.8%, 75.1% and 79.4%, respectively. These results indicate that Na2SeO3 coating can enhance the structural stability of the material surface, thereby reducing structural rearrangement during charge and discharge.

[0079] However, the discharge specific capacity of NSO-4% is only 205.3 mAh g -1 , ICE is 45.9%. This decrease in electrochemical performance can be attributed to the excessive Na2SeO3 coating that hinders the Li +Among the various samples, NSO-3% exhibits the highest specific discharge capacity and ICE, indicating that appropriate surface treatment can enhance the electrochemical performance of LRM cathode materials, which is attributed to the synergistic effect of the reduction-induced stabilization of the electrochemically active spinel interlayer and the surface coating of the material.

[0080] Figure 5 b is the first cycle cyclic voltammetry curve of the original LMR and the modified sample after coating with Na2SeO3. According to the figure, the four samples have similar CV curves in the first cycle, in which the oxidation peak at 4V corresponds to the transition metal (Ni 2+ / 4+ and Co 3+ / 4+ ) oxidation, and the oxidation peak at 4.5V belongs to the activation of the Li2MnO3 component. In addition, all the redox peaks in the first cycle CV curves of the four samples almost overlap, indicating that the stability of the surface structure of the material is improved after coating modification.

[0081] In order to further explore the effect of the spinel@Na2SeO3 coating structure on the LRM material, the cycling performance and rate performance at high current density of NSO-0, NSO-1%, NSO-2%, NSO-3% and NSO-4% samples were tested at 0.5C and 1C between 2.0-4.8V. The rate performance of the five samples at 0.1C to 10C is shown in Figure 2. Figure 5 Obviously, NSO-3% exhibits excellent rate performance compared with other samples, with discharge capacities of 276.6, 255.8, 239.2, 222.2, 184.4, 139.5, and 87.4 mAh g at 0.1-10C, respectively. -1 The excellent rate performance is due to the spinel structure with three-dimensional diffusion channels, which is beneficial to improve the Li + The transmission rate.

[0082] like Figure 5 As shown in e and 5f, after 200 cycles, the NSO-3% sample showed the best cycle stability, with a discharge capacity of 185.3 mAh g after 200 cycles at 1C. -1 , the capacity retention rate is 78.5%; the specific capacity after cycling at 0.5C is 221.6 mAh g -1 , the capacity retention rate is 86.4%. This is because the reduction-induced spinel structure has a stable 3D skeleton and has good structural compatibility with the layered phase, which can increase structural stability and further inhibit phase transition. Moreover, the outermost Na2SeO3 layer can stabilize the electrode surface structure and reduce the reaction between the active material and the electrolyte. Therefore, the synergistic effect of the Na2SeO3 protective layer and the spinel structure contributes to the improvement of cycling performance.

[0083] Voltage decay is another challenge faced by LRM materials, which is caused by irreversible lattice oxygen loss triggering phase transition. Figure 5 Figure d shows the voltage decay curves for all samples at a current density of 1C. NSO-0 exhibits a severe voltage decay of 0.6995 V after 200 cycles. In contrast, the voltage decay of the Na2SeO3-modified samples is significantly suppressed, especially the NSO-3% sample, which exhibits a voltage drop of only 0.4445 V after 200 cycles. This reduction in voltage decay can be attributed to the oxygen vacancies on the surface of the modified material, which hinder the release of lattice oxygen and improve the structural stability of the material, thereby hindering TM migration and the structural transformation from the layered phase to the spinel phase.

[0084] Example 4 Kinetic Test of Lithium-Rich Manganese-Based Materials with Different Na2SeO3 Coating Amounts

[0085] In order to further understand the electrochemical properties of NSO-3% materials, this example performed EIS tests on each sample. Figure 6 Nyquist plots of NSO-0, NSO-1%, NSO-2%, NSO-3% and NSO-4% after 3 cycles and Z' versus ω -1 / 2 The linear simulation diagram of the experimental data is Figure 6 The equivalent circuit shown in (a) is simulated, and the corresponding results are shown in Table 1.

[0086] According to the experimental results, it can be seen that the Rs and Rct values of NSO-3% are lower than those of other samples. This is due to the protective effect of the Na2SeO3 coating layer, which isolates the active material from the organic electrolyte and inhibits the occurrence of side reactions.

[0087] Lithium ion diffusion coefficient (D Li+ ) can be calculated according to formula (1):

[0088]

[0089] according to Figure 6 The linear simulation shown in (b) was used to calculate the D values of NSO-0, NSO-1%, NSO-2%, NSO-3% and NSO-4%. Li+ The values are 9.527×10 -16 , 1.550×10 -14 , 1.070×10 -14 , 1.180×10 -14 and 10.477×10 - 16 cm 2 s -1The excellent diffusion kinetics of NSO-3% is attributed to the fast lithium ion diffusion channels provided by the spinel structure. These results provide a good explanation for the excellent electrochemical performance of the NSO-3% sample, especially the excellent rate capability.

[0090] Table 1 Impedance fitting values and Li of NSO-0, NSO-1%, NSO-2%, NSO-3% and NSO-4% samples + Diffusion coefficient

[0091]

[0092] The above description is only a preferred embodiment of the present invention and is not intended to limit the present invention. Any modifications, equivalent substitutions, improvements, etc. made within the spirit and principles of the present invention should be included in the scope of protection of the present invention.

Claims

1. A method for preparing a lithium-rich manganese-based material having a spinel@Na2SeO3 structure, characterized in that: The lithium-rich manganese-based positive electrode material is mixed with sodium selenite and ground, and calcined under an argon environment to obtain the lithium-rich manganese-based material having a spinel@Na2SeO3 structure; The calcination temperature is 330°C to 370°C, and the calcination time is 2 to 4 hours; Based on the total mass after mixing being 100 wt %, the mass percentage of the sodium selenite is 3 wt %.

2. The method for preparing a lithium-rich manganese-based material having a spinel@Na2SeO3 structure according to claim 1, characterized in that: The lithium-rich manganese-based positive electrode material is Li 1.2 Mn 0.54 Ni 0.13 Co 0.13 O2 material.

3. The method for preparing a lithium-rich manganese-based material having a spinel@Na2SeO3 structure according to claim 2, characterized in that: The Li 1.2 Mn 0.54 Ni 0.13 Co 0.13 The preparation method of O2 material is co-precipitation-high temperature solid phase method.

4. The method for preparing a lithium-rich manganese-based material having a spinel@Na2SeO3 structure according to claim 3, characterized in that: The coprecipitation-high temperature solid phase method comprises the following steps: S1, prepare the mixture containing Mn 2+ 、Ni 2+ 、Co 2+ A mixed sulfate solution, a Na2CO3 solution and an ammonium bicarbonate aqueous solution; wherein the Mn 2+ 、Ni 2+ 、Co 2+ The molar ratio is 54:13:13, the total cation concentration is 2 mol / L, the concentration of the Na2CO3 solution is 2 mol / L, and the concentration of the ammonium bicarbonate aqueous solution is 0.12 mol / L; S2. Simultaneously injecting the mixed sulfate solution and the Na2CO3 solution into the preheated aqueous ammonium bicarbonate solution, stirring and reacting, and after the reaction is completed, standing and aging to obtain a product; the feed rate of the mixed sulfate solution and the Na2CO3 solution is 0.5 mL / min; and the reaction time is 15 to 17 h; S3, filtering, separating, washing, and drying the product in sequence to obtain a carbonate precursor powder; S4, mixing and grinding the precursor powder with lithium carbonate, wherein the molar ratio of the precursor powder to the lithium carbonate is 1:1.35; then pre-calcining and high-temperature calcining are performed in sequence to obtain the Li 1.2 Mn 0.54 Ni 0.13 Co 0.13 O2 material; the pre-firing temperature is 550 ℃ ~ 650 ℃, the time is 4 to 6 hours, the high temperature calcination temperature is 850 ~ 950 ℃, the time is 10 to 12 hours.

5. The method for preparing a lithium-rich manganese-based material having a spinel@Na2SeO3 structure according to claim 4, characterized in that: In step S2, the preheating temperature is 53°C to 57°C.

6. The method for preparing a lithium-rich manganese-based material having a spinel@Na2SeO3 structure according to claim 4, characterized in that: In step S2, the temperature of the static aging is 55° C. and the time is 12 hours.

7. A lithium-rich manganese-based material having a spinel@Na2SeO3 structure, characterized in that: The method is prepared by any one of claims 1 to 6.

8. A lithium-ion battery, characterized in that: It is prepared using the lithium-rich manganese-based material as claimed in claim 7.

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