Positive electrode plate, electrochemical device comprising the positive electrode plate, and electrical device

Abstract

A positive electrode plate comprising a positive electrode current collector and a positive electrode active material layer provided on at least one surface of the positive electrode current collector. The positive electrode active material layer comprises a positive electrode active material, the positive electrode active material comprising a ternary positive electrode material layer containing trace elements. The trace elements are boron, zirconium, and aluminum. the positive electrode plate satisfies the following equation: 11.0 ≤ [F 101 + (D FW / 4.5)] × 1.85 + ln (M) ≤ 17.0; in the equation is F 101 a half-width in the unit ° of a diffraction peak at a position where the diffraction angle 20 in an XRD spectrum of the positive electrode active material is 36.6 ± 1°; D FWis a half-width, in the unit µm, of the particle size volume distribution of the positive electrode active material; and M is a total mass fraction, in the unit of ppm, of the trace elements in the positive electrode active material.

Description

BACKGROUNDTechnical field

[0001] The present invention relates to the field of electrochemical technology, in particular to a positive electrode plate or a positive pole piece, an electrochemical device comprising the positive electrode plate, and an electrical device. Description of the state of the art

[0002] With the rapid development of modern science and technology, the widespread application of small electrical and electronic products and communications equipment places higher demands on battery performance. As a new generation of environmentally friendly rechargeable batteries, lithium-ion batteries have attracted increasing attention due to their high specific energy, high working voltage, long cycle life, low self-discharge, and excellent safety performance. They are used in mobile phones, portable computers, video cameras, and still cameras, and are gradually replacing traditional batteries in the fields of aviation and navigation, medical instruments, and military communications equipment.

[0003] However, as the application range of lithium-ion batteries expands, so does the demand for their performance. Among other things, high-temperature cycling performance is one of the challenges for modern electrical and electronic products. In a high-temperature environment, the battery's positive electrode material can experience thermal expansion of the lattice structure, leading to a decrease in battery capacity and an increase in internal resistance.

[0004] The currently commercially available lithium-ion positive electrode materials include lithium iron phosphate, lithium cobaltate, ternary nickel-cobalt-manganese materials, etc. Although the theoretical capacity of various positive electrode materials is not small, increasing the cut-off voltage to 4.2 V or less will increase the energy density, and there is also the problem of rapid capacity decay and excessive increase in internal resistance.

[0005] Nickel-cobalt-manganate-lithium oxide ternary positive electrode (NCM) materials, especially high-nickel ternary positive electrode materials, which exhibit high capacity and excellent energy density, are widely used as positive electrode materials in lithium-ion batteries. However, the stability of high-nickel ternary positive electrode materials limits their commercial application.

[0006] Therefore, there is a need to develop a positive electrode plate that has better cycling performance under high temperature and high voltage conditions. SUMMARY

[0007] An object of the present invention is to overcome the disadvantages of the prior art and to provide a positive electrode plate, an electrochemical device comprising the positive electrode plate, and an electrical device. It can significantly improve the internal resistance growth rate and capacity retention rate of the electrochemical device after high-temperature and high-voltage cycling after the positive electrode plate is attached to the electrochemical device. The invention is defined by the features of the independent claims. Advantageous embodiments are subject to the dependent claims.

[0008] In order to achieve the above-mentioned object, in a first aspect of the present invention, the present invention provides a positive electrode plate comprising a positive electrode current collector and a positive electrode active material layer provided on at least one surface of the positive electrode current collector, wherein the positive electrode active material layer comprises a positive electrode active material, the positive electrode active material comprises a ternary positive electrode material layer containing trace elements, and the trace elements are boron, zirconium and aluminum; the positive electrode plate satisfies the following equation: 11.0≤[F101+(DFW / 4.5)]×1.85+ln(M)≤17.0; in the following equation, F 101a half-width or half-peak width with the unit ° of a diffraction peak at a position where the diffraction angle 20 in an XRD spectrum of the positive electrode active material is 36.6 ± 1°; D FW is a half-width, with the unit µm, of the particle size volume distribution of the positive electrode active material; and M is a total mass fraction, with the unit ppm, of the trace elements in the positive electrode active material.

[0009] In a preferred embodiment of the present invention, the positive electrode plate satisfies the following equation 13.0≤[F 101 +(D FW / 4.5)]×1.85+ln(M)≤16.0.

[0010] In an alternative embodiment of the present invention, the range of F 101 between 0.2° and 1.6°.

[0011] In an alternative embodiment of the present invention, the range of F 101 between 0.8° and 1.35°.

[0012] In an alternative embodiment of the present invention, the range of D FW between 4 µm and 15 µm.

[0013] In an alternative embodiment of the present invention, the range of D FW between 8 µm and 13 µm.

[0014] In an alternative embodiment of the present invention, the range of M is between 2,500 ppm and 7,000 ppm.

[0015] In an alternative embodiment of the present invention, the range of M is between 2,800 and 5,000 ppm.

[0016] In an alternative embodiment of the present invention, the contents of B, Al and Zr in the trace elements correspond to the following equation -20≤(3×M B +1.3×M Zr -2×(M Al ) / 100≤30; in the equation are M B , M Zr and M Althe mass fractions of boron, zirconium or aluminum in the positive electrode active material with the unit ppm.

[0017] In an alternative embodiment of the present invention, the contents of B, Al and Zr in the trace elements correspond to the following equation -8≤(3×M B +1.3×M Zr -2×M Al ) / 100≤15.

[0018] In an alternative embodiment of the present invention, the mass fraction of B in the positive electrode active material is 300-1,000 ppm.

[0019] In an alternative embodiment of the present invention, the mass fraction of Zr in the positive electrode active material is 1,000-3,000 ppm.

[0020] In an alternative embodiment of the present invention, the mass fraction of Al in the positive electrode active material is 1,000-4,000 ppm.

[0021] In an alternative embodiment of the present invention, the ternary positive electrode material satisfies the formula LiNi x Co y Mn (1-x-y) O2, where 0.7≤x<1.0 <y<0,3, and 0< x+y<1.

[0022] In a second aspect, the present invention provides an electrochemical device comprising the positive electrode plate as described above.

[0023] In a third aspect, the present invention provides an electrical device comprising the electrochemical device described above.

[0024] The present invention has the following advantageous effects.

[0025] The present invention provides a positive electrode plate, an electrochemical device comprising the positive electrode plate, and an electrical device. The structural stability of the positive electrode active material at high temperatures and the cycling performance of the positive electrode plate are significantly improved by controlling the trace element content of the positive electrode active material in the positive electrode plate, the half-width of the diffraction peak at a diffraction angle 20 of about 36.6° in an XRD spectrum, and the half-width of the particle size volume distribution, so that an internal resistance growth rate and a capacity retention rate of the electrochemical device including the positive electrode plate after cycling under high-voltage and high-temperature conditions are improved. BRIEF DESCRIPTION OF THE DRAWINGS

[0026] For a better understanding of the invention, reference is made to exemplary embodiments illustrated in the following drawings. The components in the drawings are not necessarily to scale and related elements may be omitted, or in some cases, proportions may have been exaggerated so that the features described herein are emphasized and clearly illustrated. Furthermore, related elements or components may be arranged differently, as is known in the art. Furthermore, in the drawings, like reference numerals designate corresponding parts throughout the several views. For a better understanding of the invention, reference is made to exemplary embodiments illustrated in the following drawings.The components in the drawings are not necessarily to scale and related elements may be omitted or, in some cases, proportions may have been exaggerated. Fig. 1 is a typical view showing an XRD spectrum of a positive electrode active material of the present invention. DESCRIPTION OF THE DESIGNS

[0027] To clarify the objectives, technical solutions, and advantages of the embodiments of the invention, the technical solutions in the embodiments of the invention are described clearly and completely below. Of course, the described examples are only a part of the invention and not all examples. Starting from the examples of the invention, all other examples that a person skilled in the art can deduce without inventive effort are also within the scope of the invention.

[0028] The present invention includes, among the technical features described openly, both a closed technical solution consisting of the mentioned features and an open technical solution containing the mentioned features.

[0029] In the present invention, reference is made to numerical ranges, which, unless otherwise stated, are to be considered continuous and include both the minimum and maximum values of the range, as well as any value between the minimum and maximum values. When a range refers to an integer, it also includes any integer between the minimum and maximum values of the range. When multiple ranges are specified to describe a feature or characteristic, the ranges may also be combined. In other words, unless otherwise stated, all ranges disclosed herein also include all subranges contained therein.

[0030] In the present invention, the specific methods for dispersing and stirring the treatment are not particularly limited.

[0031] Unless the reagents or instruments used in the invention are specified by the manufacturer, they are commercially available products.

[0032] It should be noted that in the content of the present application, the present application is explained by taking a lithium-ion secondary battery as an example of an electrochemical device, but the electrochemical device of the present application is not limited to the lithium-ion secondary battery. Positive electrode plate

[0033] An example of the present invention provides a positive electrode plate comprising a positive electrode current collector and a positive electrode active material layer provided on at least one surface of the positive electrode current collector, wherein the positive electrode active material layer comprises a positive electrode active material, the positive electrode active material comprises a ternary positive electrode material containing trace elements, and the trace elements are boron, zirconium, and aluminum elements.

[0034] The positive electrode plate satisfies the following equation: 11.0≤[F101+(DFW / 4.5)]×1.85+ln(M)≤17.0; in the following equation, F 101 a half-width in unit ° (namely, in unit degrees) of a diffraction peak at a position where a diffraction angle 20 is 36.6 ± 1° in an XRD spectrum of the positive electrode active material; D FWis a half-width with the unit µm of the particle size volume distribution of the positive electrode active material; and M is a total mass fraction, with the unit ppm, of the trace elements in the positive electrode active material.

[0035] In the present invention, by controlling the content of trace elements in the positive electrode active material in the positive electrode plate, the half-width of the diffraction peak at a position where the diffraction angle 20 in the XRD spectrum is about 36.6°, and the half-width of the particle size volume distribution, the above-mentioned parameters are comprehensively adjusted so that the following equation is satisfied: 11.0≤[F 101 +(D FW / 4.5)]×1.85+ln(M)≤17.0, and thereby the stability and cycling performance of the positive electrode plate at high temperature and high pressure is significantly improved.

[0036] In the XRD pattern of the positive electrode active material, a diffraction peak at a diffraction angle 2θ of 36.6 ± 1° represents a characteristic diffraction peak of a (101) crystal plane of the positive electrode active material. In the R-3m point group structure of the ternary positive electrode material, the crystal lattice is formed by stacking a plurality of layered metal oxide layers, and the (101) crystal plane refers to a specific crystal plane in the crystal. Its Miller index is (101). In a layered structure, a crystal can be considered to be composed of a plurality of layers, each layer containing metal ions and oxygen atoms.

[0037] In the (101) crystal plane, the metal ions and oxygen atoms are arranged in a regular pattern, forming a (101) crystal plane structure. Since the oxygen atoms are usually located at a central position in the layered structure and their contribution to X-ray diffraction is relatively small, the intensity of the diffraction peak of the oxygen atoms is usually relatively weak. Metal ions (e.g., cobalt, nickel, manganese, etc.) contribute significantly to X-ray diffraction, and their crystal planes typically exhibit diffraction peaks of moderate intensity. In particular, the (101) crystal plane of the layered structure may exhibit an alternating arrangement of metal ions and oxygen atoms, or an arrangement of metal ions in a chain-like or honeycomb-like structure with interspersed oxygen atoms.

[0038] In this study, it was found that the half-width (F 101) of the diffraction peak at a diffraction angle 2θ of 36.6 ± 1° in the XRD pattern, that is, the half-width of the diffraction peak at the (101) crystal plane, which can reflect the crystal orientation, crystal structure and metal ion arrangement of the positive electrode active material.

[0039] From the point of view of crystal orientation, a larger value for F 101generally indicates a more complex crystal orientation. In general, the polycrystal exhibits a larger half-width of the diffraction peak of the (101) crystal plane of the positive electrode active material than the single crystal. The smaller the crystal size, the larger the half-width. The crystal orientation can be used to evaluate the orientation uniformity and degree of orientation of the positive electrode active material. The more complicated the crystal orientation, the lower the orientation uniformity and degree of orientation. After the orientation of the positive electrode active material is improved to a specific degree, the dynamic performance of the positive electrode active material, especially the high-voltage charge-discharge capacity, is significantly improved, and the good interfacial stability is maintained.However, excessive orientation exacerbates the interfacial side reaction at high temperatures, which is not conducive to the high-temperature charge-discharge stability of ternary positive electrode materials. Regarding the crystal structure, the higher the periodicity of the crystal structure of the positive electrode active material, the lower the degree of defects and the smaller the value of F. 101. It has been found that a specific degree of unit cell defects or asymmetry is beneficial for the structural stability and lithium extraction rate of the positive electrode active material and contributes to the battery's charge / discharge performance. The capacity retention rate is high, especially after high-pressure cycling. However, the structural stability of the positive electrode active material matrix is quickly destroyed by excessive defects and excessive defect accumulation, resulting in structural collapse during charging and discharging, serious deterioration of structural stability, and an excessive increase in internal resistance after high-temperature cycling. Regarding the arrangement of metal ions, a narrower half-width of the diffraction peak of the (101) crystal plane, i.e., a lower value of F 101, generally indicates that the metal atoms in the positive electrode active material layer have better order and periodicity, and the mutual stacking between the layers is also regular, which contributes to improving the stability of the battery, especially a lower growth rate of internal resistance. Therefore, the value of F 101 be within a reasonable range and neither too large nor too small.

[0040] D FWis the half-width of the particle size volume distribution of the positive electrode active material, that is, the difference between the two particle size values corresponding to half the maximum height of the interval particle size distribution curve of the positive electrode active material. The interval particle size distribution curve (also called differential particle size distribution) of the positive electrode active material is well-known in the art and is defined as a curve with particle size as the abscissa and volume percentage as the ordinate, which can more accurately represent the distribution characteristics of the positive electrode active material particles. If D FW is small, this means that the particle size distribution is relatively concentrated. If D FW is larger, the particle size distribution is wider.

[0041] At high temperatures, the positive electrode active material may experience a volume change due to thermal expansion after the battery cycle. If D FW of the positive electrode active material is too small, i.e., the particle size distribution is very concentrated, the volume change of all particles may be too uniform, resulting in stress concentration of the entire positive electrode active material. Such stress concentrations may lead to structural failure of the material and reduce the stability of the positive electrode plate. In addition, the particle size is too uniform, which is not conducive to pore filling during the densification of the electrode plate, and there is a risk of local overpressure, which hinders the migration of lithium ions in the positive electrode active material. Therefore, the positive electrode active material should have a moderate D FW have, and D FW should not be too small.

[0042] In addition, D FW should not be too large. Too large a particle size half-width means that the particle size distribution range is wide, which may lead to too large a capacity difference between individual particles, resulting in uneven capacity of the positive electrode plate during high-voltage charging and discharging, thereby accelerating the battery capacity decline and reducing the battery cycle performance. In addition, D FWof the positive electrode active material is too large, meaning there are some very large or very small particles. The large particles are inert at the interfaces, and the lithium ions inside the particles have difficulty migrating. The larger size difference between the particles leads to greater unevenness in the charging and discharging process of the positive electrode plate, resulting in local, accelerated failure, such as an excessive increase in internal resistance.

[0043] This study finds that F 101 and D FWcan comprehensively evaluate the morphology properties of positive electrode active materials at the crystal and particle levels for the positive electrode plate containing the positive electrode active materials. Considering the different influence of the properties at the crystal and particle levels on the high-temperature stability and cycling performance of the battery, a comprehensive definition and regulation in the above-mentioned relationship of "F 101 +(D FW / 4.5)”.

[0044] M is the total mass fraction of boron (B), zirconium (Zr), and aluminum (Al) in the positive electrode active material. The content of B, Zr, and Al has a specific influence on the crystal structure and interfacial stability of positive electrode active materials. The positive electrode active material contains an appropriate amount of B, Zr, and Al, which helps increase the migration rate of lithium ions in the positive electrode material, prevents the failure of the bulk crystal structure and interfacial structure caused by lithium ion penetration, eliminates the local stress generated during battery cycling, and improves high-temperature stability.However, excessive content of trace elements may cause excessive lattice defects in the positive electrode active material, locally destroy the order of the layered structure of the positive electrode active material, or hinder the intercalation and deposition of ions, resulting in degradation behavior of the positive electrode active material, such as abnormally low capacitance and high impedance.

[0045] Considering that the half-width of the diffraction peak of the (101) crystal plane is related to the crystal structure of the positive electrode active material and the arrangement of metal ions, the content of trace elements also affects the crystal lattice of the positive electrode active material. The content of B, Zr, and Al, especially Zr and Al as metal elements, as well as their fluctuations and distribution, have a special influence on the value of F 101 .

[0046] By controlling the content of B, Zr and Al and further combining F 101 with D FW Therefore, the present invention rationally controls the trace element content as well as the crystal and particle properties of the positive electrode plate, thereby improving the stability and cycle performance of the lithium-ion battery at high temperatures.

[0047] In the present invention, the value of [F 101 +(D FW / 4.5)]×1.85+ln(M) can be, for example, 11.0, 11.5, 12.0, 14.0, 16.0, 16.5 or 17.0 or an interval of two of these values.

[0048] In one of the embodiments, the positive electrode plate satisfies the following equation 13.0≤[F 101 +(D FW / 4.5)]×1.85+ln(M)≤16.0.

[0049] In one of the embodiments, the range of F 101 between 0.2° and 1.6°, e.g. 0.2°, 0.25°, 0.3°, 0.5°, 0.8°, 1.0°, 1.2°, 1.3°, 1.4°, 1.45°, 1.5° or 1.6°.

[0050] In an alternative embodiment, the range of F 101 between 0.8° and 1.35°.

[0051] In the above-mentioned alternative range of F 101 The positive electrode active material has a suitable crystal size, crystal structure and arrangement of metal ions, which contributes to improving the stability and cycling performance of the battery at high temperatures.

[0052] Regarding the method for detecting F 101 The present invention is not limited, and one skilled in the art may use an X-ray diffraction (XRD) test to determine the half-width of the diffraction peak of the (101) crystal plane of the positive electrode active material, wherein the XRD test conditions may include a method known in the art.

[0053] For F 101Control can be achieved by changing the content of trace elements, by adjusting the content and distribution of cobalt, nickel and manganese in the positive electrode active material or by adjusting the preparation process of the positive electrode active material.

[0054] In one of the embodiments, the area of D FW between 4 µm and 15 µm, e.g. 4 µm, 5 µm, 6 µm, 8 µm, 10 µm, 12 µm, 13 µm, 14 µm or 15 µm.

[0055] In one of the embodiments, the area of D FW between 8 µm and 13 µm.

[0056] If D FWwithin the above-mentioned scope of the present invention, the positive electrode active material has a suitable particle size distribution range and particle gradation, which contributes to ensuring the uniformity of the reaction of the positive electrode plate during charging and discharging of the battery, thereby reducing local excessive lithium intercalation and interfacial side reactions, improving the charge / discharge performance of the battery, and improving cycle stability and structural stability.

[0057] The method for determining D FW is not limited within the scope of the present invention. The person skilled in the art is able to FWof the positive electrode active material using conventional technical means. For example, a laser particle size analyzer, such as a Master Sizer 3000 laser particle size analyzer from Malvern Instruments Ltd. in the UK, can be used.

[0058] The regulation of D FWThe screening of positive electrode active materials generally uses a sorting and sieving process. The specific screening and sieving method is not particularly limited and can be selected according to the situation. Generally, mesh sieves are used for screening and sieving. The positive electrode active material is usually sieved through sieves with different mesh sizes. Due to the different particle sizes, particles with a small particle size are sorted out by the sieves, while particles with the desired particle size are retained on the sieves. This results in positive electrode active materials with different particle sizes. Active substances with special particle size dimensions can be formulated as needed, so their particle size distribution can be manually adjusted.

[0059] In one of the embodiments, the range of M is between 2,500 ppm and 7,000 ppm, e.g. 2,500 ppm, 2,700 ppm, 3,000 ppm, 3,500 ppm, 4,000 ppm, 5,000 ppm, 6,000 ppm, 6,500 ppm, 6,800 ppm or 7,000 ppm.

[0060] In an alternative embodiment, the range of M is between 2,800 and 5,000 ppm.

[0061] The method for determining M is not limited within the scope of the present invention. One skilled in the art can determine the B, Zr, and Al content in positive electrode active materials using conventional technical means. Detection can be performed, for example, using the ICP test.

[0062] As for B, Zr, and Al, they can be introduced through the raw materials used in the preparation of the positive electrode active material. They can also be introduced by adding a boron source, a zirconium source, or an aluminum source during the preparation of the positive electrode active material.

[0063] Optionally, the boron source comprises boron oxide and / or boric acid. The zirconium source comprises at least one of zirconium hydroxide, zirconium nitrate, zirconium sulfate, zirconium oxide, zirconium phosphate, and zirconium chloride. The aluminum source comprises at least one of aluminum hydroxide, aluminum oxide, aluminum nitrate, aluminum acetate, aluminum sulfate, sodium aluminate, and potassium aluminate.

[0064] In one of the embodiments, the contents of B, Al and Zr in the trace elements satisfy the following equation -20≤(3×M B +1.3×M Zr -2×M Al ) / 100≤30; in the equation are M B , M Zr and M Al the mass fractions of B, Zr and Al in the positive electrode active material with the unit ppm

[0065] A specific amount of B contributes to increasing the electrical conductivity and ion diffusion rate of the material, improving the charge / discharge performance of the battery. B also forms a B-O bond with oxygen (O) in the material, with higher bond energy and stronger stability, which can improve the reversibility of the crystal phase transition and the stability of the crystal structure to a certain extent. Furthermore, B is more likely to form a dense coating layer evenly distributed on the surface of the material, thus isolating the physical contact between the positive electrode material and the electrolyte solution, thereby improving the growth rate of the battery's internal resistance at high temperatures.Due to the larger ionic radius of Zr, a specific amount of Zr in the positive electrode active material can expand the lithium ion diffusion channel, thereby improving the reversible discharge capacity of the material and slowing the capacity decrease of the positive electrode active material at high temperatures. Al has a smaller ionic radius (generally smaller than a Co ion and a Ni ion). Aluminum ions can form closer bonds with the surrounding oxygen ions. By controlling the Al content, the connecting force between the bonds in the positive electrode active material can be increased to improve the material's stability at high temperatures and high voltages. However, if the amounts of B, Zr, and Al are too high, impurities may be generated. In particular, the Al content can have a strong impact on the order of the crystal structure and also destroy the layered structure of the matrix material.

[0066] This study has shown that in the present application, when the content of B, Zr and Al is further controlled to satisfy a following equation -20≤(3×M B +1.3×M Zr -2×M Al ) / 100≤30, B, Zr and Al are within a reasonable range, and the growth rate of internal resistance is lower and the capacity retention rate is higher after cycling at high temperature and high pressure.

[0067] In the present invention, the value of (3×M B +1.3×M Zr -2×M Al ) / 100 can be, for example, -20, -18, -15, -10, -5, 0, 5, 10, 15, 20, 25, 28, 30, or an interval between two of the above values.

[0068] In an alternative embodiment, the contents of B, Al and Zr in the trace elements correspond to the following equation -8≤(3×M B +1.3×M Zr -2×M Al ) / 100≤15.

[0069] In one embodiment, the mass fraction of B in the positive electrode active material is 300-1,000 ppm.

[0070] In an alternative embodiment, the mass fraction of B in the positive electrode active material is 500-900 ppm.

[0071] In one embodiment, the mass fraction of Zr in the positive electrode active material is 1,000-3,000 ppm.

[0072] In an alternative embodiment, the mass fraction of Zr in the positive electrode active material is 1,100-1,800 ppm.

[0073] In one embodiment, the mass fraction of Al in the positive electrode active material is 1,000-4,000 ppm.

[0074] In an alternative embodiment, the mass fraction of Al in the positive electrode active material is 1,200-2,500 ppm.

[0075] In one embodiment, the ternary positive electrode material has the following formula LiNi x Co y Mn(1-x-y) O2, where 0.7≤x<1, 0 <y<0,3, and 0<x+y<1.

[0076] In the present invention, the method for preparing LiNi x Co y Mn (1-x-y) O2 is not limited. A person skilled in the art can prepare a positive electrode active material according to conventional technical methods. For example, the positive electrode active material precursor and the lithium source are mixed and subjected to a sintering treatment to obtain a positive electrode active material. The sintering treatment may, for example, comprise multiple sintering steps, including primary and secondary sintering. The steps of cooling, ball milling, etc. may also be included between the primary sintering and the secondary sintering.

[0077] The precursor of the positive electrode active material may be one or more oxides, hydroxides, and carbonates containing Ni, Co, and Mn in a stoichiometric ratio, for example, hydroxides containing Ni, Co, and Mn in a stoichiometric ratio. The precursor of the positive electrode active material can be obtained by a method known in the art, e.g., by a coprecipitation method, a gel method, or a solid-phase method.

[0078] For example, a Ni source, a Co source, and a Mn source are dispersed in a solvent to obtain a mixed solution. The mixed solution, the strong base solution, and the complexing agent solution are simultaneously pumped into a stirred reaction vessel, with the pH of the reaction solution controlled at 10-13 and the temperature in the reaction vessel at 25-90°C. The mixture is protected by an inert gas during the reaction. After the reaction is complete, aging, filtration, washing, and vacuum drying are performed to obtain a hydroxide containing Ni, Co, and Mn.

[0079] In some examples of the invention, the Ni source comprises at least one of nickel sulfate, nickel nitrate, nickel chloride, nickel oxalate, or nickel acetate; and / or the Co source comprises at least one of cobalt sulfate, cobalt nitrate, cobalt chloride, cobalt oxalate, or cobalt acetate; and / or the Mn source comprises at least one of manganese sulfate, manganese nitrate, manganese chloride, manganese oxalate, or manganese acetate; and / or the Li source comprises at least one of lithium oxide (Li2O), lithium phosphate (Li3PO4), lithium dihydrogen phosphate (LiH2PO4), lithium acetate (CH3COOLi), lithium hydroxide (LiOH), lithium carbonate (Li2CO3), or lithium nitrate (LiNO3).

[0080] The positive electrode active material precursor and the lithium source can be mixed using a ball mill mixer or a high-speed mixer. The mixed material is placed in an atmospheric sintering furnace for sintering. The sintering atmosphere is an oxygen-containing atmosphere, such as air or oxygen.

[0081] In addition, the positive electrode active material can also be subjected to a coating process. Specifically, a coating material is applied to the surface of the positive electrode active material by dry coating (high-temperature solid-state process). The surface of the positive electrode active material is partially or completely covered with a coating layer formed by the coating material.

[0082] In addition to the positive electrode active material, the positive electrode active material layer may comprise a conductive agent and a binder.

[0083] The conductive agent is used to ensure the electrical conductivity of the electrode. Any conductive agent can be used without particular restrictions, as long as it has suitable electronic conductivity without causing adverse chemical changes in the battery. This preferably includes carbon fibers such as carbon nanofibers, carbon black such as acetylene black and Ketjen black, and carbon materials such as activated carbon, graphite, mesoporous carbon, fullerenes, and carbon nanotubes.

[0084] The binder improves the adhesion between the particles of the positive electrode active material and the adhesion between the positive electrode active material and the current collector. Suitable binders for use in embodiments are fluoropolyolefin-based binders, which may include, but are not limited to, polyvinylidene fluoride (PVDF), vinylidene fluoride copolymers, or modified (e.g., modified by carboxylic acid, acrylic acid, acrylonitrile, etc.) derivatives thereof, and the like.

[0085] In the present invention, the positive electrode current collector is not particularly limited as long as it has electrical conductivity without causing adverse chemical changes in the battery. This includes, for example, stainless steel, aluminum, nickel, titanium, burnt carbon, or aluminum or stainless steel whose surface has been treated with any of carbon, nickel, titanium, silver, etc.

[0086] The positive electrode plate in the present invention can be prepared by conventional methods in the art. For example, a positive electrode active material, a conductive agent, and a binder are dispersed in a solvent. The solvent can be N-methylpyrrolidone (NMP) or deionized water to form a uniform positive electrode slurry. The positive electrode slurry is applied to a positive electrode current collector. After drying, rolling, and the like, a positive electrode plate is obtained. Electrochemical device

[0087] According to one example of the present invention, an electrochemical device is provided comprising the positive electrode plate as described above, a negative electrode plate or a negative pole piece and an electrolyte solution or an electrolyte.

[0088] The negative electrode plate of the present invention comprises a negative electrode current collector and a negative electrode active material layer provided on at least one surface of the negative electrode current collector. The negative electrode active material comprises a negative electrode active material and may also comprise conductive agents and / or binders.

[0089] The negative electrode current collector is not particularly limited in the present invention, as long as it has high conductivity without causing adverse chemical changes in the battery. For example, copper, stainless steel, aluminum, nickel, titanium, burnt carbon, copper or stainless steel surface-treated with one of carbon, nickel, titanium, silver, or the like, or an aluminum-cadmium alloy can be used.

[0090] Regarding the negative electrode active material, the type of the negative electrode active material in the examples of the present invention is not specifically limited and can be selected according to practical requirements. The negative electrode active material can be, for example, one or more of the following materials: natural graphite, artificial graphite, mesophase carbon microspheres (MCMB), hard carbon, soft carbon, silicon, silicon-carbon composite, SiOm (0 <m<2, z.B. m=1), Li-Sn-Legierung, Li-Sn-O-Legierung, Sn, SnO, SnO2, spinell-strukturiertes Lithiumtitanat Li4Ti5O 12 , Li-Al alloy and metallic lithium

[0091] The examples of the present invention do not specifically limit the types of the conductive agent and the binder in the negative electrode active material layer, and they can be selected according to practical requirements. The conductive agent is, for example, one or more of the following materials: graphite, superconducting carbon, acetylene black, carbon black, Ketjen black, carbon dots, carbon nanotubes, graphene, and carbon nanofibers. The binder is one or more of styrene-butadiene rubber, polyvinylidene fluoride, polytetrafluoroethylene, polyvinyl butyral, aqueous acrylic resin, and carboxymethyl cellulose. The negative electrode active material layer may optionally also comprise a thickener such as carboxymethyl cellulose.

[0092] The electrolyte solution of the present invention may be any electrolyte solution known in the art for use in electrochemical energy storage devices. The electrolyte solution comprises an electrolyte and a solvent. The electrolyte solution may generally comprise a lithium salt.

[0093] Specifically, the lithium salt comprises at least one of lithium hexafluorophosphate (LiPF6), lithium tetrafluoroborate (LiBF4), lithium perchlorate (LiClO4), lithium hexafluoroarsenate (LiAsF6), lithium bisfluorosulfonimide (LiFSI), lithium bistrifluoromethosulfonimide (LiTFSI), lithium triflate (LiTFS), lithium difluorooxalate borate (LiDFOB), lithium dioxalate borate (LiBOB), lithium difluorophosphate (LiPO2F2), lithium difluorooxalate phosphate (LiDFOP), and lithium tetrafluorooxalate phosphate (LiTFOP). The concentration of the electrolyte in the electrolyte solution can be 0.5 to 5 mol / L.

[0094] Specifically, the solvent includes at least one of ethylene carbonate (EC), propylene carbonate (PC), ethyl methyl carbonate (EMC), diethyl carbonate (DEC), dimethyl carbonate (DMC), dipropyl carbonate (DPC), methyl propyl carbonate (MPC), ethyl propyl carbonate (EPC), butylene carbonate (BC), fluoroethylene carbonate (FEC), methyl formate (MF), methyl acetate (MA), ethyl acetate (EA), propyl acetate (PA), methyl propionate (MP), ethyl propionate (EP), propyl propionate (PP), methyl butyrate (MB), ethyl butyrate (EB), 1,4-butyrolactone (GBL), sulfolane (SF), dimethyl sulfone (MSM), methyl ethyl sulfone (EMS), and diethyl sulfone (ESE). The solvent may be contained in an amount of 70 to 98 wt% based on the weight of the electrolyte solution.

[0095] Furthermore, the electrolyte solution may comprise additives. In particular, the additive may include a membrane-forming additive for the negative electrode or negative electrode plate, and the additive may include a membrane-forming additive for the positive electrode or positive electrode plate. The additive may include an additive capable of improving specific properties of the battery, e.g., an additive for improving the overcharge characteristics of the battery, an additive for improving the high-temperature characteristics of the battery, or an additive for improving the low-temperature characteristics of the battery, etc.

[0096] The electrochemical device may further comprise a separator disposed between the positive electrode plate and the negative electrode plate to separate the positive electrode plate and the negative electrode plate from each other and prevent the positive electrode plate and the negative electrode plate from contacting and causing a short circuit. The separator may be any material known in the art that can be used as a separator for electrochemical energy storage devices. In particular, the separator comprises at least one of polyethylene, polypropylene, polyvinylidene fluoride, aramid, polyethylene terephthalate, polytetrafluoroethylene, polyacrylonitrile, polyimide, polyamide, polyester, and natural fiber. Electrical device

[0097] Examples of the present invention provide an electrical device comprising the electrochemical device described above. The electrochemical device serves as a power supply for the electrical device.

[0098] The electric device refers to any device that can use electrical energy and convert it into mechanical energy, heat energy, light energy, etc., such as an electric motor, an electric heat engine, an electric light source, etc. The electric device may specifically include, but is not limited to, a mobile device, an electric vehicle, an electric train, a ship and a satellite, an energy storage system, etc. The mobile device may be a mobile phone, a notebook computer, an unmanned aerial vehicle or drone, a sweeping robot, an electric cigarette, etc. The electric vehicle may be a pure electric vehicle, a hybrid electric vehicle, a plug-in hybrid electric vehicle, an electric bicycle, an electric scooter, an electric golf cart, an electric truck, or the like.

[0099] The invention is further illustrated by the following specific examples. Example 1

[0100] This Example 1 provides a lithium-ion battery, and the specific preparation method is as follows. (1) Preparation of the positive electrode plate

[0101] (1.1) According to the molar ratio of the individual elements Li, Ni, Co and Mn in the chemical formula LiNi 0,91 Co 0,02 Mn 0,07 Nickel sulfate, cobalt sulfate, manganese sulfate, and lithium hydroxide were weighed in a solution of O2. Lithium hydroxide was present in slight excess. The ratio of the molar amount of lithium hydroxide to the total molar amount of nickel sulfate, cobalt sulfate, and manganese sulfate (Li / Me) was 1.05:1.

[0102] (1.2) Nickel sulfate, cobalt sulfate, and manganese sulfate were each dissolved in deionized water. Each metal solution was transferred to a reaction vessel through a pipe to form a mixed metal solution, with nitrogen introduced as a protective gas. An aqueous NaOH solution was added to the mixed metal solution as a precipitating agent and ammonia as a complexing agent. The ammonia concentration was gradually adjusted to control the pH of the solution between 10 and 13. The temperature of the reaction vessel was controlled at 50 and 55°C. The reaction lasted for 10 hours to obtain a ternary precursor after aging, filtration, washing, and vacuum drying.

[0103] (1.3) Lithium hydroxide and a ternary precursor containing a boron source (boron oxide), a zirconium source (zirconium hydroxide), and an aluminum source (aluminum oxide) were mixed. The addition amount of the boron source, the zirconium source, or the aluminum source was adjusted so that M B , M Zr and M Almet the requirements listed in Table 2. The mixture was subjected to primary sintering. The sintering atmosphere was an oxygen-containing atmosphere with an O2 concentration of 90%. The temperature and time of the primary sintering are given in Table 1. After cooling, the sintered product was placed in a ball mill for ball milling. The temperature, time, and rotation speed of the ball milling are given in Table 1. The ball milled product was then secondary sintered in an oxygen-containing atmosphere with an O2 concentration of 90%. The temperature and time of the secondary sintering are given in Table 1.

[0104] (1.4) The sintered material was ground, crushed and sieved after secondary sintering to obtain a ternary positive electrode active material that met the requirements of D FW in Table 2.

[0105] (1.5) The positive electrode active material, a binder (polyvinylidene fluoride), and a conductive agent (carbon black) were mixed in a mass ratio of 97:1:2. N-methylpyrrolidone (NMP) was added to the mixture and stirred under the action of a vacuum stirrer until the mixed system formed into a positive electrode slurry with uniform fluidity. The positive electrode slurry was evenly coated on the positive electrode current collector (aluminum foil). The positive electrode current collector coated with the positive electrode slurry was transferred to an oven for drying and then rolled and cut to obtain a positive electrode plate. (2) Manufacturing the negative electrode plate

[0106] (1.2) A negative electrode active material (artificial graphite), a conductive agent (acetylene black), a thickener (carboxymethyl cellulose, CMC), and a binder (styrene-butadiene rubber, SBR) were mixed in a mass ratio of 97:12:1:1. A negative electrode slurry was prepared by a wet method using a vacuum stirrer. The negative electrode slurry was evenly coated on a negative electrode current collector (copper foil). The negative electrode current collector coated with the negative electrode slurry was transferred to a furnace for drying and then rolled and cut to obtain a negative electrode plate. (3) Preparation of the electrolyte solution

[0107] Ethylene carbonate (EC), ethyl methyl carbonate (EMC), and diethyl carbonate (DEC) were mixed in a volume ratio of 20:20:60 to obtain an organic solvent, and then sufficient dried lithium salt LiPF6 was dissolved in the mixed organic solvent to prepare an electrolyte solution with a concentration of 1 mol / L. (4) Preparation of the separator

[0108] A 12 µm thick polypropylene release film was used. (5) Preparation of the battery

[0109] The prepared positive electrode plate, separator, and negative electrode plate were wound to obtain a bare electrical core without liquid injection. The bare electrical core was placed in an outer packaging film. The above-mentioned prepared electrolyte solution was injected into the dried bare electrical core. The same was subjected to vacuum packaging, standing, molding, sorting, and other processes to obtain a lithium-ion battery. Examples 2-18 and comparative examples 1-5

[0110] Examples 2-18 and Comparative Examples 1-5 each provide a lithium-ion battery whose preparation method is similar to that of Example 1, except that in the preparation of a positive electrode plate, the addition amount of a boron source, a zirconium source, or an aluminum source was adjusted so that M B , M Zr and M Almet the requirements shown in Table 2. The temperature and time of primary sintering, the temperature, time and rotation speed of ball milling (it should be noted that in Examples 4 and 12, the ball milling step was not carried out, i.e., after cooling the primary sintered product, secondary sintering is carried out directly), and the temperature and time of secondary sintering are shown in Table 1. After secondary sintering, the material was ground, crushed and sieved so that D FW meets the requirements shown in Table 2. Table 1 Primary sintering Ball milling Secondary sintering Temperature (°C) Duration (hours) Temperature (°C) Duration (hours) Rotational speed (rpm) Temperature (°C) Duration (hours) Example 1 830 8 25 0,75 25 450 4 Example 2 850 9 25 1 30 500 4 Example 3 800 7 30 1 40 450 6 Example 4 870 8 / / / 430 4 Example 5 850 8 25 0,75 40 450 3 Example 6 780 7,5 35 2 35 450 4 Example 7 800 8 45 0,5 25 470 3 Example 8 810 7,5 25 0,5 45 460 5 Example 9 880 7,5 45 0,75 40 420 3 Example 10 750 9 30 0,5 30 430 5 Example 11 900 9 45 1 40 450 5 Example 12 920 9 / / / 400 4 Example 13 750 8,5 40 0,75 30 460 5 Example 14 860 8,5 45 1,25 35 425 5 Example 15 815 7 25 0,3 50 470 4 Example 16 710 8 45 2 40 400 3 Example 17 910 9 40 1,75 35 400 4 Example 18 880 10 45 1,75 30 430 5 Compare Example 1 950 10 40 2 35 430 5 Compare Example 2 730 7,5 25 0,5 30 425 3,5 Compare Example 3 845 9 35 1,25 30 455 5 Compare Example 4 755 8 30 1 35 410 3,5 Compare Example 5 915 8 30 1,25 30 410 3,5

[0111] For each example and comparative example, the trace element content (i.e. the value of M, comprising M B , M Zr and M Al ) of the positive electrode plate, and F 101of the positive electrode active material, and the above test methods were as follows.

[0112] M: The lithium-ion battery was disassembled to obtain a positive electrode plate. The positive electrode plate was soaked in dimethyl carbonate (DMC) at room temperature for 60 minutes. The positive electrode plate was taken out and dried at room temperature with a humidity of ≤ 15%. The positive electrode active material layer on the surface of the current collector was scraped off to perform calcination at 500°C for 3 hours to remove the conductive agent, the binder, the surface-side reaction products, and the residual electrolyte solution. After washing and drying, the positive electrode active material was obtained. 2 g of the positive electrode active material was used for ICP determination using an ICP tester (ICAP 7400) to obtain the mass contents of B, Zr, and Al in the positive electrode active material, which were respectively expressed as M B , M Zr and M Al , M=M B +MZr +M Al , recorded in ppm.

[0113] D FW: The lithium-ion battery was disassembled to obtain a positive electrode plate. The positive electrode plate was soaked in DMC at room temperature for 60 minutes. The positive electrode plate was taken out and dried at room temperature with a humidity of ≤ 15%. The positive active material layer on the surface of the current collector was scraped off to perform calcination at 500°C for 3 hours to remove the conductive agent, binder, surface-side reaction products, and residual electrolyte solution. The positive active material was obtained after washing and drying. The positive electrode active material was dispersed in an aqueous solution containing 3% sodium hexametaphosphate as a dispersant. The resultant was continuously stirred with a glass rod for 10 cycles.Then, the sample was quickly poured into a sample basin of a particle size distribution measuring device (Master Sizer 3000 laser particle size analyzer, manufactured by Malvern Instruments Ltd., UK) to determine D. FW with the unit µm.

[0114] F 101: The lithium-ion battery was disassembled to obtain a positive electrode plate. The positive electrode plate was soaked in DMC at room temperature for 60 minutes. The positive electrode was removed and dried at room temperature with a humidity of ≤ 15%. The positive active material layer on the surface of the current collector was scraped off to perform calcination at 500°C for 3 hours to remove the conductive agent, binder, surface-side reaction products, and residual electrolyte solution. The positive active material was obtained after washing and drying. 2 g of the positive electrode active material was used for an XRD test using X-ray diffraction (Rigaku Ultima IV-type X-ray diffractometer from Rigaku). The specific test conditions were as follows: Cu target, scan voltage 40 kV, current 40 mA, scan range 10-90° and scan rate 10 ° / min.X-ray diffraction was calibrated by the internal silicon standard method. The diffraction peak at the position where the diffraction angle 2° in the XRD pattern was 36.6 ± 1° was the diffraction peak of the (101) crystal plane, and the half-width of this diffraction peak was F. 101 with the unit °.

[0115] In each of the examples and comparative examples, M (including M B , M Zr and M Al ) and D FW , F 101 Test results of the positive electrode active material are shown in Table 2. The XRD spectrum of the positive electrode active material of Example 1 was Fig. 1, which was a typical graph of the XRD spectrum of the positive electrode active material of the present invention. Table 2 F 101 (°) D FW (µm) M (ppm) M B (ppm) M Zr (ppm) M Al (ppm) Example 1 1,22 12,6 3520 784 1205 1531 Example 2 1,03 10,5 4214 336 1827 2051 Example 3 1,11 10,5 4204 307 1511 2386 Example 4 0,89 10,3 4195 905 2069 1221 Example 5 1,08 10,6 4222 781 1785 1656 Example 6 1,35 8,1 4841 792 1586 2463 Example 7 0,82 11,6 2806 410 1189 1207 Example 8 1,15 12,8 4942 815 2068 2059 Example 9 0,93 8,5 2917 459 1138 1320 Example 10 1,4 10,3 2659 311 1053 1295 Example 11 0,68 7,2 6867 852 2726 3289 Example 12 0,31 14,5 4963 521 2114 2328 Example 13 1,35 12,9 4984 713 1839 2432 Example 14 0,81 8,0 2804 405 1220 1179 Example 15 1,13 14,6 6935 817 2905 3213 Example 16 1,58 4,1 2561 351 1180 1030 Example 17 0,23 6,8 2913 537 1150 1226 Example 18 0,42 6,7 3003 885 1092 1026 Comparative Example 1 0,22 4,3 2945 330 1082 1533 Comparative Example 2 1,60 15,2 7069 1059 3120 2890 Comparative Example 3 0,92 9,6 5939 0 2830 3109 Comparative Example 4 1,46 11,9 3447 696 0 2751 Comparative Example 5 0,57 7,5 3167 527 2640 0

[0116] The lithium-ion batteries manufactured in the examples and comparative examples were subjected to performance tests according to the following projects and methods. (1) Growth rate of internal resistance:

[0117] After conventional formation to a constant volume, the prepared lithium-ion battery was charged at 45°C to 4.5 V at a constant current of 0.33 C and then charged at a constant voltage to a current of ≤ 0.05 C and switched off to obtain a capacity Q0. After a standstill time of 5 minutes, the battery was discharged with an electrical quantity of 0.5 Q0 (i.e., 50% SOC) at 0.33 C, leaving 10 minutes and recording the voltage as V1. It was then discharged for 18 seconds at 1 C, recording the voltage as V2, then (V1-V2) / 1 C, thus obtaining the internal resistance DCR1 of the cyclic lithium-ion battery. The above steps were repeated for the same lithium-ion battery, recording the internal resistance DCR 200 of the lithium-ion battery after the 200th cycle. The growth rate of the internal resistance of the lithium-ion battery = (DCR 200-DCR1) / DCR1×100%, with the unit %. (2) Capacity maintenance rate:

[0118] S1. The lithium-ion battery was placed in an environment of 25°C, standing until the lithium-ion battery reached a constant temperature, charged to 4.4 V at a constant current of 0.33C, and then discharged to 2.8 V at 25°C, standing for 60 minutes.

[0119] S2. Then, the lithium-ion battery was placed in an environment standing at 65°C until the lithium-ion battery reached a constant temperature, charged to 4.5 V at a constant current of 0.33 C, and charged at a constant voltage to a current of ≤ 0.05 C, and discharged to 2.8 V at 0.33 C after 5 minutes of standing, taking this capacity as the initial capacity C1.

[0120] S3. Step S2 was repeated for 200 cycles and the capacity of 200 cycles was recorded as C 200recorded. The capacity maintenance rate was calculated by the capacity maintenance rate = C 200 / C1 × 100%.

[0121] According to Table 2, the calculation results of [F 101 +(D FW / 4.5)]×1.85+ln(M) and (3×M B +1.3×M Zr -2×M Al ) / 100 and the results of the lithium-ion battery performance tests are shown in Table 3 below Table 3 [F 101 +(D FW / 4,5)]×1,85+ ln(M) (3×M B +1,3×M Zr -2×M Al ) / 100 Growth rate of internal resistance Capacity maintenance rate Example 1 15,60 8,57 31,50% 92,70% Example 2 14,57 -7,19 33,60% 92,50% Example 3 14,71 -18,87 38,40% 91,20% Example 4 14,22 29,63 37,50% 91,10% Example 5 14,70 13,52 35,10% 93,10% Example 6 14,31 -4,88 31,80% 92,90% Example 7 14,23 3,62 32,40% 93,50% Example 8 15,90 10,15 33,30% 92,80% Example 9 13,19 2,16 34,50% 91,80% Example 10 14,71 -2,88 40,20% 90,20% Example 11 13,05 -4,78 41,10% 89,80% Example 12 15,04 -3,45 42,60% 90,50% Example 13 16,31 -3,34 48,60% 87,70% Example 14 12,73 4,43 46,20% 88,30% Example 15 16,94 -1,99 49,60% 86,60% Example 16 12,46 5,27 52,90% 85,50% Example 17 11,20 6,54 50,80% 86,10% Example 18 11,54 20,23 51,40% 85,30% Compare Example 1 10,16 -6,69 70,80% 77,00% Compare Example 2 18,07 14,53 75,30% 78,30% Compare Example 3 14,34 -25,39 65,40% 79,60% Compare Example 4 15,74 -34,14 67,20% 78,70% Compare Example 5 12,20 50,13 66,00% 79,90%

[0122] With respect to the lithium-ion battery prepared in each embodiment of the present invention, the internal resistance growth rate under high-temperature and high-voltage conditions after 200 cycles was ≤53%, and the capacity retention rate was ≥85%. It can be seen that the stability of the lithium-ion battery containing the positive electrode plate of the present invention is significantly improved under high-temperature and high-voltage conditions, the internal resistance growth rate of the lithium-ion battery is low, and the capacity retention rate is high.

[0123] From Examples 2 to 5, it is clear that the capacity retention rate and the growth rate of internal resistance of the lithium-ion battery are relatively better when the contents of boron element, zirconium element and aluminum element are - 20≤(3×M B +1.3×M Zr -2×M Al ) / 100≤30.

[0124] As can be seen from Comparative Examples 1 to 5, the growth rate of internal resistance and capacity retention rate of the lithium-ion battery after cycling under high voltage and high temperature are poor when the value of the positive electrode plate [F 101 +(D FW / 4.5)]×1.85+ln(M) is outside the range of the invention or no boron, zirconium or aluminum is contained in the positive electrode active material.

Claims

[1] A positive electrode plate comprising a positive electrode current collector and a positive electrode active material layer provided on at least one surface of the positive electrode current collector, characterized by that the positive electrode active material layer comprises a positive electrode active material, wherein the positive electrode active material comprises a ternary positive electrode material layer containing trace elements; the trace elements are boron, zirconium, and aluminum; the positive electrode plate satisfies the following equation: 11.0≤[F101+(DFW / 4.5)]×1.85+ln(M)≤17.0; in the equation is F 101 a half-width in the unit ° of a diffraction peak at a position where the diffraction angle 20 in an XRD spectrum of the positive electrode active material is 36.6 ± 1°; D FWis a half-width, in the unit µm, of the particle size volume distribution of the positive electrode active material; and M is a total mass fraction, in the unit of ppm, of the trace elements in the positive electrode active material. [2] Positive electrode plate according to claim 1, characterized by that the positive electrode plate satisfies the following equation 13.0≤[F101+(DFW / 4.5)]×1.85+ln(M)≤16.

0. [3] Positive electrode plate according to one of the preceding claims, characterized by that a range of F 101 from 0.2° to 1.6°. [4] Positive electrode plate according to one of the preceding claims, characterized by that a range of F 101 from 0.8° to 1.35°. [5] Positive electrode plate according to one of the preceding claims, characterized by that an area of D FW from 4 µm to 15 µm. [6] Positive electrode plate according to one of the preceding claims, characterized by that an area of D FW between 8 µm and 13 µm. [7] Positive electrode plate according to one of the preceding claims, characterized by that a range of M lies between 2,500 ppm and 7,000 ppm. [8] Positive electrode plate according to one of the preceding claims, characterized by that a range of M lies between 2,800 ppm and 5,000 ppm. [9] Positive electrode plate according to one of the preceding claims, characterized by that the contents of B, Al and Zr in the trace elements satisfy the equation −20≤(3×MB+1.3×MZr−2×MA1) / 100≤30 where in the equation M B , M Zr and M Al Mass fractions in the unit ppm of boron, zirconium or aluminum in the positive electrode active material. [10] Positive electrode plate according to one of the preceding claims, characterized by that the content of B, Al and Zr in the trace elements satisfies the equation - 8≤(3×M B+1.3×M Zr -2×M Al ) / 100≤15 is met. [11] Positive electrode plate according to one of the preceding claims, characterized by , that (a) the mass fraction of boron in the positive electrode active material is 300-1,000 ppm. [12] Positive electrode plate according to one of the preceding claims, characterized by , that (b) the mass fraction of zirconium in the positive electrode active material is 1,000-3,000 ppm. [13] Positive electrode plate according to one of the preceding claims, characterized by , that (c) the mass fraction of aluminum in the positive electrode active material is 1,000-4,000 ppm. [14] Positive electrode plate according to one of the preceding claims, characterized by that the ternary positive electrode material has the formula LiNixCoyMn(1−x−y)O2 fulfilled, where 0.7 <x<1, 0<y<0,3, und 0<x+y<1. [15] The positive electrode plate according to claim 14, wherein 0.91≤x<1. [16] Positive electrode plate according to one of the preceding claims, wherein the positive electrode current collector comprises stainless steel, aluminum, nickel, titanium, calcined carbon, or aluminum. [17] Positive electrode plate according to one of the preceding claims, wherein the positive electrode active material layer comprises, in addition to the positive electrode active material, a conductive agent and a binder. [18] Positive electrode plate according to claim 17, wherein the conductive agent comprises carbon fibers, carbon black and / or carbon materials. [19] Positive electrode plate according to claim 17 or 18, wherein the binder is a fluoropolyolefin-based binder. [20] Electrochemical device, in particular lithium-ion battery, characterized by that it comprises the positive electrode plate according to one of claims 1 to 19. [21] An electrochemical device according to claim 20, comprising a negative electrode plate and an electrolyte solution or electrolyte. [22] Electrochemical device according to claim 20 or 21, wherein the negative electrode plate comprises a negative electrode current collector and a negative electrode active material layer provided on at least one surface of the negative electrode current collector, and wherein the negative electrode active material layer comprises a negative electrode active material. [23] Electrochemical device according to claim 22, wherein copper, stainless steel, aluminum, nickel, titanium, burnt carbon or an aluminum-cadmium alloy is intended or used for the negative electrode current collector. [24] Electrochemical device according to claim 22 or 23, wherein the negative electrode active material comprises one or more of the following materials: natural graphite, artificial graphite, mesophase carbon microspheres (MCMB), hard carbon, soft carbon. [25] Electrochemical device according to one of claims 22 to 24, wherein the negative electrode active material comprises one or more of the following materials: silicon, silicon-carbon composite, SiOm with 0 <m<2, z.B. m=1. [26] Electrochemical device according to one of claims 22 to 25, wherein the negative electrode active material comprises one or more of the following materials: Li-Al alloy and metallic lithium. [27] Electrochemical device according to one of claims 22 to 26, wherein the negative electrode active material comprises one or more of the following materials: spinel-structured lithium titanate Li4Ti5O 12, Li-Sn alloy, Li-Sn-O alloy, Sn, SnO and SnO2. [28] Electrochemical device according to one of claims 22 to 27, wherein the negative electrode active material comprises a conductive agent. [29] Electrochemical device according to claim 28, wherein the conductive agent of the negative electrode plate comprises one or more of graphite, superconducting carbon, acetylene black, carbon black, Ketjen black, carbon dots, carbon nanotubes, graphene, and carbon nanofibers. [30] Electrochemical device according to one of claims 22 to 29, wherein the negative electrode active material comprises a binder. [31] Electrochemical device according to claim 30, wherein the binder of the negative electrode plate comprises one or more of styrene-butadiene rubber, polyvinylidene fluoride, polytetrafluoroethylene, polyvinyl butyral, aqueous acrylic resin, and carboxymethyl cellulose. [32] Electrochemical device according to one of claims 22 to 31, wherein the negative electrode active material layer comprises a thickener, e.g. carboxymethylcellulose. [33] Electrochemical device according to any one of claims 21 to 32, wherein the electrolyte solution comprises an electrolyte and a solvent. [34] Electrochemical device according to one of claims 21 to 33, wherein the electrolyte comprises a lithium salt. [35] Electrochemical device according to claim 34, wherein the lithium salt comprises at least one of lithium hexafluorophosphate or LiPF6, lithium tetrafluoroborate or LiBF4, lithium perchlorate or LiClO4, lithium hexafluoroarsenate or LiAsF6, lithium bisfluorosulfonimide or LiFSI, lithium bis-trifluoromethosulfonimide or LiTFSI, lithium triflate or LiTFS, lithium difluorooxalate borate or LiDFOB, lithium dioxalate borate or LiBOB, lithium difluorophosphate or LiPO2F2, lithium difluorooxalate phosphate or LiDFOP and lithium tetrafluorooxalate phosphate or LiTFOP. [36] Electrochemical device according to any one of claims 21 to 35, where the concentration of the electrolyte in the electrolyte solution is 0.5 to 5 mol / L. [37] Electrochemical device according to one of claims 33 to 36, wherein the solvent comprises at least one of ethylene carbonate or EC, propylene carbonate or PC, ethyl methyl carbonate or EMC, diethyl carbonate or DEC, dimethyl carbonate or DMC, dipropyl carbonate or DPC, methyl propyl carbonate or MPC, ethyl propyl carbonate or EPC, butylene carbonate or BC, fluoroethylene carbonate or FEC, methyl formate or MF, methyl acetate or MA, ethyl acetate or EA, propyl acetate or PA, methyl propionate or MP, ethyl propionate or EP, propyl propionate or PP, methyl butyrate or MB, ethyl butyrate or EB, 1,4-butyrolactone or GBL, sulfolane or SF, dimethyl sulfone or MSM, methyl ethyl sulfone or EMS and diethyl sulfone or ESE. [38] Electrochemical device according to one of claims 33 to 37, wherein the solvent is contained in an amount of 70 to 98 wt.% based on the weight of the electrolyte solution. [39] Electrochemical device according to one of claims 21 to 38, wherein the electrolyte solution comprises a membrane-forming additive for the negative electrode plate and a membrane-forming additive for the positive electrode plate. [40] Electrochemical device according to one of claims 21 to 39, comprising a separator between the positive electrode plate and the negative electrode plate. [41] Electrochemical device according to claim 40, wherein the separator comprises at least one of the following materials: polyethylene, polypropylene, polyvinylidene fluoride, aramid, polyethylene terephthalate, polytetrafluoroethylene, polyacrylonitrile, polyimide, polyamide, polyester and natural fiber. [42] An electrochemical device according to any one of claims 20 to 41 for use in supplying power to an electrical device, the electrical device comprising: Electric motor, heat engine, light source, vehicle, train, ship, satellite, energy storage system, mobile phone, notebook, unmanned aerial vehicle, sweeping robot, or electric cigarette. [43] The electrochemical device of claim 42, wherein the vehicle is a pure electric vehicle, a hybrid electric vehicle, a plug-in hybrid electric vehicle, an electric bicycle, an electric scooter, an electric golf cart, or an electric truck. [44] Electrical device, characterized by that it comprises the electrochemical device according to one of claims 20 to 43. [45] Electrical device according to claim 44, wherein the electrochemical device serves as a power supply for the electrical device. [46] An electrical device according to claim 45, which is configured as an electric motor, heat engine, light source, vehicle, train, ship, satellite, energy storage system, mobile phone, notebook, unmanned aerial vehicle, sweeping robot, or electric cigarette. [47] Electrical device according to claim 46, where the vehicle is a pure electric vehicle, a hybrid electric vehicle, a plug-in hybrid electric vehicle, an electric bicycle, an electric scooter, an electric golf cart, or an electric truck.

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