WO2023173403A1 - 高镍三元正极材料及其制备方法、二次电池、电池模块、电池包和用电装置 - Google Patents

高镍三元正极材料及其制备方法、二次电池、电池模块、电池包和用电装置 Download PDF

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WO2023173403A1
WO2023173403A1 PCT/CN2022/081676 CN2022081676W WO2023173403A1 WO 2023173403 A1 WO2023173403 A1 WO 2023173403A1 CN 2022081676 W CN2022081676 W CN 2022081676W WO 2023173403 A1 WO2023173403 A1 WO 2023173403A1
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nickel ternary
cathode material
ternary cathode
nickel
battery
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PCT/CN2022/081676
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French (fr)
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沈重亨
吴奇
桓书星
罗东升
柳娜
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宁德时代新能源科技股份有限公司
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Priority to CN202280022589.8A priority Critical patent/CN117099225A/zh
Priority to PCT/CN2022/081676 priority patent/WO2023173403A1/zh
Priority to EP22902462.5A priority patent/EP4276945A1/en
Publication of WO2023173403A1 publication Critical patent/WO2023173403A1/zh

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    • C—CHEMISTRY; METALLURGY
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    • C—CHEMISTRY; METALLURGY
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    • C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
    • C01G53/00—Compounds of nickel
    • C01G53/40—Nickelates
    • C01G53/42—Nickelates containing alkali metals, e.g. LiNiO2
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M10/00—Secondary cells; Manufacture thereof
    • H01M10/05—Accumulators with non-aqueous electrolyte
    • H01M10/052—Li-accumulators
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M10/00—Secondary cells; Manufacture thereof
    • H01M10/05—Accumulators with non-aqueous electrolyte
    • H01M10/052—Li-accumulators
    • H01M10/0525—Rocking-chair batteries, i.e. batteries with lithium insertion or intercalation in both electrodes; Lithium-ion batteries
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/13—Electrodes for accumulators with non-aqueous electrolyte, e.g. for lithium-accumulators; Processes of manufacture thereof
    • H01M4/131—Electrodes based on mixed oxides or hydroxides, or on mixtures of oxides or hydroxides, e.g. LiCoOx
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    • H01M4/36—Selection of substances as active materials, active masses, active liquids
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    • H01M4/36—Selection of substances as active materials, active masses, active liquids
    • H01M4/362—Composites
    • H01M4/366—Composites as layered products
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/36—Selection of substances as active materials, active masses, active liquids
    • H01M4/48—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides
    • H01M4/52—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides of nickel, cobalt or iron
    • H01M4/525—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides of nickel, cobalt or iron of mixed oxides or hydroxides containing iron, cobalt or nickel for inserting or intercalating light metals, e.g. LiNiO2, LiCoO2 or LiCoOxFy
    • C—CHEMISTRY; METALLURGY
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    • C01P2002/52—Solid solutions containing elements as dopants
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
    • C01P2004/00—Particle morphology
    • C01P2004/54—Particles characterised by their aspect ratio, i.e. the ratio of sizes in the longest to the shortest dimension
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
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    • C01P2004/60—Particles characterised by their size
    • C01P2004/61—Micrometer sized, i.e. from 1-100 micrometer
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    • C01—INORGANIC CHEMISTRY
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    • C01P2006/21—Attrition-index or crushing strength of granulates
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M2004/021—Physical characteristics, e.g. porosity, surface area
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M2004/026—Electrodes composed of, or comprising, active material characterised by the polarity
    • H01M2004/028—Positive electrodes
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
    • Y02E60/10—Energy storage using batteries

Definitions

  • the present application relates to the technical field of lithium batteries, and in particular to a high-nickel ternary cathode material and its preparation method, secondary batteries, battery modules, battery packs and electrical devices.
  • lithium-ion secondary batteries are widely used in energy storage power systems such as hydraulic, thermal, wind and solar power stations, as well as power tools, electric bicycles, and electric motorcycles. , electric vehicles, military equipment, aerospace and other fields.
  • lithium-ion secondary batteries have achieved great development, higher requirements have been placed on their energy density, cycle performance and safety performance.
  • High-nickel cathode active materials are considered the best choice to meet high energy density requirements.
  • nickel content continues to increase, its structural stability becomes worse and worse, which in turn affects the cycle performance and storage performance of lithium-ion secondary batteries.
  • This application was made in view of the above-mentioned issues, and its purpose is to provide a high-nickel ternary cathode material so that the lithium-ion secondary battery prepared therefrom has good cycle performance and storage stability at high temperatures.
  • this application provides a high-nickel ternary cathode material and a preparation method thereof, a secondary battery, a battery module, a battery pack and an electrical device.
  • the first aspect of this application provides a high-nickel ternary cathode material, including
  • the matrix Li 1+x Ni a Co b Mg c Y d M (1-abcd) O 2 ⁇ y , M is selected from at least one of Mn, Zr, Al, B, Ta, Mo, W, Nb, Sb, and La species, among which: 0.8 ⁇ a ⁇ 1.0, 0 ⁇ b ⁇ 0.2, 0 ⁇ c ⁇ 0.005, 0 ⁇ d ⁇ 0.01, a+b+c+d ⁇ 1, -0.5 ⁇ x ⁇ 0.5, 0 ⁇ y ⁇ 0.02 , the surface of the substrate is provided with a coating layer, and the coating layer contains a boron-containing alloy.
  • the Y element and the Mg element are uniformly distributed in the outer particles of the material powder.
  • the Y element helps to form the outer radial rod-shaped particles and helps improve the isotropy of stress change.
  • the Mg element has Helps to ease the severity of the H2-H3 phase transition, inhibits the dramatic changes in unit cell volume during deep charge and discharge, thereby inhibiting the expansion of intra- and inter-granular cracks; at the same time, the boron-containing alloy covering the grain boundaries can absorb the grain boundaries The accumulated stress fatigue can also protect the active surface from corrosion by electrolyte by-products, thereby improving the cycle performance and storage stability of secondary batteries at high temperatures.
  • the boron-containing alloy is M'B z , where M' is selected from at least one of Co, Ti, Zr, W, Al, and Mo, and 0 ⁇ z ⁇ 4.
  • M' is selected from at least one of Co, Ti, Zr, W, Al, and Mo, and 0 ⁇ z ⁇ 4.
  • c 0 ⁇ c ⁇ 0.003.
  • c is within the given range, it helps to improve the structural stability of the high-nickel ternary cathode material under drastic changes in unit cell volume without affecting the gram capacity too much.
  • d 0 ⁇ d ⁇ 0.005.
  • d is within the given range, it helps to improve the particle arrangement order and radial distribution of the high-nickel ternary cathode material and suppress intragranular cracks without causing the specific surface area of the surface particles to be too large to cause excessive Side effects.
  • the coating amount of the boron-containing alloy is 1000 ppm-15000 ppm, based on the total weight of the metal elements in the boron-containing alloy relative to the matrix.
  • the coating amount of the boron-containing alloy is within the given range, the strength of the grain boundaries can be maximized without reducing capacity due to clogging of pores.
  • the particle size Dv 50 of the high-nickel ternary cathode material is 3 ⁇ m-18 ⁇ m, optionally 9 ⁇ m-14 ⁇ m, and the volume distribution distance (Dv 90 -Dv 10 )/Dv 50 ⁇ 1.30.
  • the volume distribution diameter of the high-nickel ternary cathode material is within the given range, the compaction density of the sintered high-nickel ternary cathode material can be increased, thereby further increasing the volume energy density of the ternary cathode material.
  • the BET of the high-nickel ternary cathode material is 0.2m 2 /g-1m 2 /g, optionally 0.3m 2 /g-0.7m 2 /g.
  • the corrosion of the electrolyte can be reduced, thereby improving the storage performance of the secondary battery.
  • the tap density TD of the high-nickel ternary cathode material is 1.8g/cm 3 -2.5g/cm 3 , optionally 1.9g/cm 3 -2.3g/cm 3 .
  • the processing performance of the high-nickel ternary cathode material can be improved.
  • the second aspect of the application also provides a method for preparing a high-nickel ternary cathode material, including the following steps:
  • High nickel ternary cathode materials include
  • the matrix Li 1+x Ni a Co b Mg c Y d M (1-abcd) O 2 ⁇ y , M is selected from at least one of Mn, Zr, Al, B, Ta, Mo, W, Nb, Sb, and La species, among which: 0.8 ⁇ a ⁇ 1.0, 0 ⁇ b ⁇ 0.2, 0 ⁇ c ⁇ 0.005, 0 ⁇ d ⁇ 0.01, a+b+c+d ⁇ 1, -0.5 ⁇ x ⁇ 0.5, 0 ⁇ y ⁇ 0.02 , the surface of the substrate is provided with a coating layer, and the coating layer contains a boron-containing alloy.
  • the method of the present application can obtain a high-nickel ternary cathode material with a precursor having a radial distribution structure and outer particles rich in Y and Mg elements.
  • the method of the present application has two processes of nucleation and nucleation growth in step S2, which can synthesize a radially distributed shell structure on the core, and can significantly improve the long-term performance of the sintered high-nickel ternary cathode material.
  • the method of this application is divided into two schemes in step S4: sintering in a low-temperature inert atmosphere and sintering in a high-temperature oxygen atmosphere.
  • the former can maximize the advantages of boron-containing alloys, and the latter can realize the reaction of the alloy with residual lithium and stabilize the surface. Lattice oxygen.
  • the inert atmosphere is nitrogen (N 2 ) or argon (Ar 2 ) with a purity of 99.9% or higher.
  • step S4 the sintering temperature is 300°C-650°C.
  • step S4 the sintering time is 3h-10h.
  • the particle size of the boron-containing alloy is 50 nm-3200 nm.
  • a third aspect of the application provides a secondary battery, including the high-nickel ternary cathode material of the first aspect of the application or the high-nickel ternary cathode material prepared according to the method of the second aspect of the application.
  • a fourth aspect of the present application provides a battery module, including the secondary battery of the third aspect of the present application.
  • a fifth aspect of the present application provides a battery pack, including the battery module of the fourth aspect of the present application.
  • a sixth aspect of the present application provides an electrical device, including at least one selected from the secondary battery of the third aspect of the present application, the battery module of the fourth aspect of the present application, or the battery pack of the fifth aspect of the present application. kind.
  • the battery modules, battery packs and electrical devices of the present application include the secondary battery of the present application, and thus have at least the same advantages as the secondary battery.
  • FIG. 1 is a schematic diagram of a secondary battery according to an embodiment of the present application.
  • FIG. 2 is an exploded view of the secondary battery according to the embodiment of the present application shown in FIG. 1 .
  • FIG. 3 is a schematic diagram of a battery module according to an embodiment of the present application.
  • Figure 4 is a schematic diagram of a battery pack according to an embodiment of the present application.
  • FIG. 5 is an exploded view of the battery pack according to an embodiment of the present application shown in FIG. 4 .
  • FIG. 6 is a schematic diagram of a power consumption device using a secondary battery as a power source according to an embodiment of the present application.
  • Ranges disclosed herein are defined in terms of lower and upper limits. A given range is defined by selecting a lower limit and an upper limit that define the boundaries of the particular range. Ranges defined in this manner may be inclusive or exclusive of the endpoints, and may be arbitrarily combined, that is, any lower limit may be combined with any upper limit to form a range. For example, if ranges of 60-120 and 80-110 are listed for a particular parameter, understand that ranges of 60-110 and 80-120 are also expected. Furthermore, if the minimum range values 1 and 2 are listed, and if the maximum range values 3, 4, and 5 are listed, then the following ranges are all expected: 1-3, 1-4, 1-5, 2- 3, 2-4 and 2-5.
  • the numerical range “a-b” represents an abbreviated representation of any combination of real numbers between a and b, where a and b are both real numbers.
  • the numerical range “0-5" means that all real numbers between "0-5" have been listed in this article, and "0-5" is just an abbreviation of these numerical combinations.
  • a certain parameter is an integer ⁇ 2
  • the method includes steps (a) and (b), which means that the method may include steps (a) and (b) performed sequentially, or may include steps (b) and (a) performed sequentially.
  • steps (c) means that step (c) may be added to the method in any order, for example, the method may include steps (a), (b) and (c), also It may include steps (a), (c) and (b), or may also include steps (c), (a) and (b), etc.
  • condition "A or B” is satisfied by any of the following conditions: A is true (or exists) and B is false (or does not exist); A is false (or does not exist) and B is true (or exists) ; Or both A and B are true (or exist).
  • the present application proposes a high-nickel ternary cathode material, including
  • the matrix Li 1+x Ni a Co b Mg c Y d M (1-abcd) O 2 ⁇ y , M is selected from at least one of Mn, Zr, Al, B, Ta, Mo, W, Nb, Sb, and La species, among which, 0.8 ⁇ a ⁇ 1.0, 0 ⁇ b ⁇ 0.2, 0 ⁇ c ⁇ 0.005, 0 ⁇ d ⁇ 0.01, a+b+c+d ⁇ 1, -0.5 ⁇ x ⁇ 0.5, 0 ⁇ y ⁇ 0.02 , the surface of the substrate is provided with a coating layer, and the coating layer contains a boron-containing alloy.
  • the deformation stacking fault rate is conducive to the same frequency of grain volume changes during the cycle, reducing the stress interaction between particles and inhibiting the expansion of intergranular cracks;
  • Mg element can deintercalate a large amount of lithium in high-nickel ternary cathode materials It provides a pillar function to inhibit the dramatic changes in unit cell volume, reduce the degree of H2-H3 phase transition, inhibit the stress-strain effect, thereby inhibiting the expansion of intragranular cracks; at the same time, the boron-containing alloy covered at the grain boundary can
  • the boron-containing alloy is M'B z , where M' is selected from at least one of Co, Ti, Zr, W, Al, and Mo, and 0 ⁇ z ⁇ 4.
  • M' is selected from at least one of Co, Ti, Zr, W, Al, and Mo, and 0 ⁇ z ⁇ 4.
  • c 0 ⁇ c ⁇ 0.003, for example, 0.0005 ⁇ c ⁇ 0.003, 0.001 ⁇ c ⁇ 0.003, 0.0005 ⁇ c ⁇ 0.001.
  • c is within the given range, it helps to improve the structural stability of the high-nickel ternary cathode material under drastic changes in unit cell volume without affecting the gram capacity too much.
  • d is within the given range, it helps to improve the particle arrangement order and radial distribution of the high-nickel ternary cathode material and suppress intragranular cracks without causing the specific surface area of the surface particles to be too large to cause excessive Side effects.
  • the coating amount of the boron-containing alloy is 1000 ppm-15000 ppm, based on the total weight of the metal elements in the boron-containing alloy relative to the matrix.
  • the coating amount of the boron-containing alloy is within the given range, the strength of the grain boundaries can be maximized without reducing capacity due to clogging of pores.
  • the particle size Dv 50 of the high-nickel ternary cathode material is 3 ⁇ m-18 ⁇ m, optionally 9 ⁇ m-14 ⁇ m, and the volume distribution distance (Dv 90 -Dv 10 )/Dv 50 ⁇ 1.30.
  • the volume distribution diameter of the high-nickel ternary cathode material is within the given range, the compacted density of the sintered high-nickel ternary cathode material can be increased, thereby further increasing the volumetric energy density of the high-nickel ternary cathode material.
  • Dv 10 is the particle size that reaches 10% of the cumulative volume from the small particle size side in the volume-based particle size distribution of powder particles, and the unit is usually ⁇ m.
  • Dv 50 is the particle size that reaches 50% of the cumulative volume from the small particle size side in the volume-based particle size distribution of powder particles.
  • Dv 90 is the particle size that reaches 90% of the cumulative volume from the small particle size side in the volume-based particle size distribution of powder particles.
  • the testing methods for the particle volume distribution sizes Dv 10 , Dv 50 , and Dv 90 of the above-mentioned ternary precursor can be tested using methods known in the art. As an example, you can refer to GB/T 19077-2016/ISO 13320:2009 Particle Size Distribution Laser Diffraction Method, using the equipment Malvern 3000 for measurement.
  • the BET of the high-nickel ternary cathode material is 0.2m 2 /g-1m 2 /g, optionally 0.3m 2 /g-0.7m 2 /g.
  • the corrosion of the electrolyte can be reduced, thereby improving the storage performance of the secondary battery.
  • the specific surface area BET of the high-nickel ternary cathode material can be tested using methods known in the art.
  • the tap density TD of the high-nickel ternary cathode material is 1.8g/cm 3 -2.5g/cm 3 , optionally 1.9g/cm 3 -2.3g/cm 3 .
  • the processing performance of the high-nickel ternary cathode material can be improved.
  • the tap density TD of the high-nickel ternary cathode material can be tested using methods known in the art.
  • the Y element is enriched on the surface of the outer particles of the powder, causing it to evolve along the radial direction, causing the aspect ratio of the primary particles in the outer layer to increase, and the aspect ratio of the primary particles is 3 -9.
  • the present application proposes a method for preparing high-nickel ternary cathode materials, including the following steps:
  • High nickel ternary cathode materials include
  • the matrix Li 1+x Ni a Co b Mg c Y d M (1-abcd) O 2 ⁇ y , M is selected from at least one of Mn, Zr, Al, B, Ta, Mo, W, Nb, Sb, and La species, among which: 0.8 ⁇ a ⁇ 1.0, 0 ⁇ b ⁇ 0.2, 0 ⁇ c ⁇ 0.005, 0 ⁇ d ⁇ 0.01, a+b+c+d ⁇ 1, -0.5 ⁇ x ⁇ 0.5, 0 ⁇ y ⁇ 0.02 , the surface of the substrate is provided with a coating layer, and the coating layer contains a boron-containing alloy.
  • the method of the present application can avoid migrating to the Li layer due to the ionic radius of heteroatoms during sintering, thereby failing to function as a pillar of the TM layer; a radially distributed structure can be obtained
  • the precursor and outer particles are high-nickel ternary cathode materials rich in Y and Mg elements.
  • the method of the present application has two processes of nucleation and nucleation growth in step S2, which can synthesize a radially distributed shell structure on the core, and can significantly improve the long-term performance of the sintered high-nickel ternary cathode material.
  • step S4 sintering in a low-temperature inert atmosphere and sintering in a high-temperature oxygen atmosphere.
  • the former can form a uniform boron-containing alloy coating layer to further strengthen the toughness of the grain boundaries, and the latter can realize the alloy Lattice oxygen that reacts with residual lithium and stabilizes the surface.
  • step S1 a mixed metal salt solution of Ni, Co and M is prepared using nickel salt, cobalt salt, M-containing compound and pure water.
  • nickel salts, cobalt salts and M-containing compounds There are no special restrictions on the types of nickel salts, cobalt salts and M-containing compounds, and can be selected according to actual needs.
  • nickel salts include one or more of nickel sulfate, nickel nitrate, and nickel acetate
  • cobalt salts include one or more of cobalt sulfate, cobalt oxalate, cobalt nitrate, and cobalt acetate
  • M manganese
  • the manganese compound includes one or more of manganese sulfate, manganese nitrate, and manganese acetate
  • the zirconium-containing compound includes one or more of zirconium dioxide, lithium zirconate, and zirconium chloride
  • M When M is aluminum, the aluminum-containing compound includes one or more of aluminum oxide, aluminum hydroxide, and lithium aluminate
  • when M is boron the boron-containing compound includes diboron trioxide, boric acid, lithium borate, boron
  • the tantalum the tantalum-containing compound includes one
  • the molybdenum-containing compound includes one or more of molybdenum dioxide, molybdenum trioxide, sodium molybdate, lithium molybdate, molybdenum anhydride, and molybdenum chloride; when M is tungsten, the tungsten-containing compound Including one or more of tungsten trioxide, sodium tungstate, lithium tungstate, ammonium tungstate; when M is niobium, the niobium-containing compound includes niobium pentoxide, niobium trioxide, niobium fluoride, chloride One or more of niobium and lithium niobate; when M is antimony, the antimony-containing compound includes one or more of antimony trioxide, antimony pentoxide, and lithium fluorantimonate; when M is lanthanum When the lanthanum-containing compound includes one or more of lanthanum trioxide, lanthanum chloride
  • step S1 the concentration of the mixed metal salt solution of Ni, Co and M is 1-5 mol/L.
  • the yttrium salt includes one or more of yttrium sulfate, yttrium nitrate, yttrium oxalate, yttrium acetate, and yttrium chloride.
  • Magnesium salts include one or more of magnesium sulfate, magnesium nitrate, magnesium oxalate, magnesium acetate, and magnesium chloride.
  • step S1 the concentration of the yttrium salt solution and the magnesium salt solution is 1-5 mol/L.
  • the alkali solution is, for example, sodium hydroxide solution with a concentration of 1-10 mol/L; the pH value is 9.5-10.5; the concentration of ammonia solution is 1-5 mol/L; the ammonia concentration is 0.5 -1mol/L, optional 0.65-0.75mol/L; reaction temperature is 65-85°C; stirring rate is 150rpm-350rpm.
  • the inert gas includes high purity (>99.9%) nitrogen and argon.
  • a high-nickel ternary precursor with an average volume distribution particle size Dv 50 of 3 ⁇ m to 18 ⁇ m can be continuously and stably obtained.
  • the ammonia concentration and reaction temperature it is beneficial to form a high-nickel ternary precursor crystal structure with good primary grain stacking and low stacking fault rate.
  • the stirring rate high-nickel ternary precursors with dense particles and uniform porosity can be synthesized while avoiding the breakage of large particles.
  • the lithium-containing compound may be lithium hydroxide, lithium carbonate, or lithium nitrate.
  • step S3 the molar ratio of lithium in the lithium-containing compound to the sum of nickel, cobalt, and M in the ternary precursor is (0.9-1.1):1.
  • the sintering temperature is 700-900°C; the sintering time is 10h-20h; and the sintering atmosphere is air or oxygen.
  • the inert atmosphere is nitrogen (N 2 ) or argon (Ar 2 ) with a purity of more than 99.9%.
  • the sintering temperature is 300°C-650°C.
  • step S4 the sintering time is 3h-10h.
  • the particle size of the boron-containing alloy is 50 nm-3200 nm.
  • a secondary battery is provided.
  • a secondary battery typically includes a positive electrode plate, a negative electrode plate, an electrolyte and a separator.
  • active ions are inserted and detached back and forth between the positive and negative electrodes.
  • the electrolyte plays a role in conducting ions between the positive and negative electrodes.
  • the isolation film is placed between the positive electrode piece and the negative electrode piece. It mainly prevents the positive and negative electrodes from short-circuiting and allows ions to pass through.
  • the positive electrode sheet includes a positive electrode current collector and a positive electrode film layer disposed on at least one surface of the positive electrode current collector.
  • the positive electrode film layer includes the high-nickel ternary positive electrode material of the first aspect of the present application.
  • the positive electrode current collector has two surfaces facing each other in its own thickness direction, and the positive electrode film layer is disposed on any one or both of the two opposite surfaces of the positive electrode current collector.
  • the positive electrode current collector may be a metal foil or a composite current collector.
  • the metal foil aluminum foil can be used.
  • the composite current collector may include a polymer material base layer and a metal layer formed on at least one surface of the polymer material base layer.
  • the composite current collector can be formed by forming metal materials (aluminum, aluminum alloys, nickel, nickel alloys, titanium, titanium alloys, silver and silver alloys, etc.) on polymer material substrates (such as polypropylene (PP), polyterephthalate It is formed on substrates such as ethylene glycol ester (PET), polybutylene terephthalate (PBT), polystyrene (PS), polyethylene (PE), etc.).
  • PP polypropylene
  • PBT polybutylene terephthalate
  • PS polystyrene
  • PE polyethylene
  • the positive electrode film layer optionally further includes a binder.
  • the binder may include polyvinylidene fluoride (PVDF), polytetrafluoroethylene (PTFE), vinylidene fluoride-tetrafluoroethylene-propylene terpolymer, vinylidene fluoride-hexafluoropropylene-tetrafluoroethylene At least one of ethylene terpolymer, tetrafluoroethylene-hexafluoropropylene copolymer and fluorine-containing acrylate resin.
  • the positive electrode film layer optionally further includes a conductive agent.
  • the conductive agent may include at least one of superconducting carbon, acetylene black, carbon black, Ketjen black, carbon dots, carbon nanotubes, graphene and carbon nanofibers.
  • the positive electrode sheet can be prepared by dispersing the above-mentioned components for preparing the positive electrode sheet, such as positive active material, conductive agent, binder and any other components in a solvent (such as N -methylpyrrolidone) to form a positive electrode slurry; the positive electrode slurry is coated on the positive electrode current collector, and after drying, cold pressing and other processes, the positive electrode piece can be obtained.
  • a solvent such as N -methylpyrrolidone
  • the negative electrode sheet includes a negative electrode current collector and a negative electrode film layer disposed on at least one surface of the negative electrode current collector, where the negative electrode film layer includes a negative electrode active material.
  • the negative electrode current collector has two opposite surfaces in its own thickness direction, and the negative electrode film layer is disposed on any one or both of the two opposite surfaces of the negative electrode current collector.
  • the negative electrode current collector may be a metal foil or a composite current collector.
  • the composite current collector may include a polymer material base layer and a metal layer formed on at least one surface of the polymer material base material.
  • the composite current collector can be formed by forming metal materials (copper, copper alloy, nickel, nickel alloy, titanium, titanium alloy, silver and silver alloy, etc.) on a polymer material substrate (such as polypropylene (PP), polyterephthalate It is formed on substrates such as ethylene glycol ester (PET), polybutylene terephthalate (PBT), polystyrene (PS), polyethylene (PE), etc.).
  • PP polypropylene
  • PBT polybutylene terephthalate
  • PS polystyrene
  • PE polyethylene
  • the negative active material may be a negative active material known in the art for batteries.
  • the negative active material may include at least one of the following materials: artificial graphite, natural graphite, soft carbon, hard carbon, silicon-based materials, tin-based materials, lithium titanate, and the like.
  • the silicon-based material may be selected from at least one of elemental silicon, silicon oxide compounds, silicon carbon composites, silicon nitrogen composites and silicon alloys.
  • the tin-based material may be selected from at least one of elemental tin, tin oxide compounds and tin alloys.
  • the present application is not limited to these materials, and other traditional materials that can be used as battery negative electrode active materials can also be used. Only one type of these negative electrode active materials may be used alone, or two or more types may be used in combination.
  • the negative electrode film layer optionally further includes a binder.
  • the binder can be selected from styrene-butadiene rubber (SBR), polyacrylic acid (PAA), polysodium acrylate (PAAS), polyacrylamide (PAM), polyvinyl alcohol (PVA), sodium alginate (SA), poly At least one of methacrylic acid (PMAA) and carboxymethyl chitosan (CMCS).
  • the negative electrode film layer optionally further includes a conductive agent.
  • the conductive agent may be selected from at least one of superconducting carbon, acetylene black, carbon black, Ketjen black, carbon dots, carbon nanotubes, graphene and carbon nanofibers.
  • the negative electrode film layer optionally includes other auxiliaries, such as thickeners (such as sodium carboxymethylcellulose (CMC-Na)) and the like.
  • thickeners such as sodium carboxymethylcellulose (CMC-Na)
  • the negative electrode sheet can be prepared by dispersing the above-mentioned components for preparing the negative electrode sheet, such as negative active materials, conductive agents, binders and any other components in a solvent (such as deionized water) to form a negative electrode slurry; the negative electrode slurry is coated on the negative electrode current collector, and after drying, cold pressing and other processes, the negative electrode piece can be obtained.
  • a solvent such as deionized water
  • the electrolyte plays a role in conducting ions between the positive and negative electrodes.
  • the type of electrolyte in this application can be selected according to needs.
  • the electrolyte can be liquid, gel, or completely solid.
  • the electrolyte is an electrolyte solution.
  • the electrolyte solution includes electrolyte salts and solvents.
  • the electrolyte salt may be selected from the group consisting of lithium hexafluorophosphate, lithium tetrafluoroborate, lithium perchlorate, lithium hexafluoroarsenate, lithium bisfluorosulfonimide, lithium bistrifluoromethanesulfonimide, trifluoromethane At least one of lithium sulfonate, lithium difluorophosphate, lithium difluoroborate, lithium dioxaloborate, lithium difluorodioxalate phosphate and lithium tetrafluoroxalate phosphate.
  • the solvent may be selected from the group consisting of ethylene carbonate, propylene carbonate, methylethyl carbonate, diethyl carbonate, dimethyl carbonate, dipropyl carbonate, methylpropyl carbonate, ethylpropyl carbonate, Butylene carbonate, fluoroethylene carbonate, methyl formate, methyl acetate, ethyl acetate, propyl acetate, methyl propionate, ethyl propionate, propyl propionate, methyl butyrate, ethyl butyrate At least one of ester, 1,4-butyrolactone, sulfolane, dimethyl sulfone, methyl ethyl sulfone and diethyl sulfone.
  • the electrolyte optionally further includes additives.
  • additives may include negative electrode film-forming additives, positive electrode film-forming additives, and may also include additives that can improve certain properties of the battery, such as additives that improve battery overcharge performance, additives that improve battery high-temperature or low-temperature performance, etc.
  • the secondary battery further includes a separator film.
  • a separator film There is no particular restriction on the type of isolation membrane in this application. Any well-known porous structure isolation membrane with good chemical stability and mechanical stability can be used.
  • the material of the isolation membrane can be selected from at least one of glass fiber, non-woven fabric, polyethylene, polypropylene and polyvinylidene fluoride.
  • the isolation film can be a single-layer film or a multi-layer composite film, with no special restrictions. When the isolation film is a multi-layer composite film, the materials of each layer can be the same or different, and there is no particular limitation.
  • the positive electrode piece, the negative electrode piece and the separator film can be made into an electrode assembly through a winding process or a lamination process.
  • the secondary battery may include an outer packaging.
  • the outer packaging can be used to package the above-mentioned electrode assembly and electrolyte.
  • the outer packaging of the secondary battery may be a hard shell, such as a hard plastic shell, an aluminum shell, a steel shell, etc.
  • the outer packaging of the secondary battery may also be a soft bag, such as a bag-type soft bag.
  • the material of the soft bag may be plastic, and examples of the plastic include polypropylene, polybutylene terephthalate, polybutylene succinate, and the like.
  • FIG. 1 shows a square-structured secondary battery 5 as an example.
  • the outer package may include a housing 51 and a cover 53 .
  • the housing 51 may include a bottom plate and side plates connected to the bottom plate, and the bottom plate and the side plates enclose a receiving cavity.
  • the housing 51 has an opening communicating with the accommodation cavity, and the cover plate 53 can cover the opening to close the accommodation cavity.
  • the positive electrode piece, the negative electrode piece and the isolation film can be formed into the electrode assembly 52 through a winding process or a lamination process.
  • the electrode assembly 52 is packaged in the containing cavity.
  • the electrolyte soaks into the electrode assembly 52 .
  • the number of electrode assemblies 52 contained in the secondary battery 5 can be one or more, and those skilled in the art can select according to specific actual needs.
  • secondary batteries can be assembled into battery modules, and the number of secondary batteries contained in the battery module can be one or more. Those skilled in the art can select the specific number according to the application and capacity of the battery module.
  • FIG. 3 is a battery module 4 as an example.
  • a plurality of secondary batteries 5 may be arranged in sequence along the length direction of the battery module 4 .
  • the plurality of secondary batteries 5 can be fixed by fasteners.
  • the battery module 4 may further include a housing having a receiving space in which a plurality of secondary batteries 5 are received.
  • the above-mentioned battery modules can also be assembled into a battery pack.
  • the number of battery modules contained in the battery pack can be one or more. Those skilled in the art can select the specific number according to the application and capacity of the battery pack.
  • the battery pack 1 may include a battery box and a plurality of battery modules 4 disposed in the battery box.
  • the battery box includes an upper box 2 and a lower box 3 .
  • the upper box 2 can be covered with the lower box 3 and form a closed space for accommodating the battery module 4 .
  • Multiple battery modules 4 can be arranged in the battery box in any manner.
  • the present application also provides an electrical device, which includes at least one of the secondary battery, battery module, or battery pack provided by the present application.
  • the secondary battery, battery module, or battery pack may be used as a power source for the electrical device, or may be used as an energy storage unit for the electrical device.
  • the electric device may include mobile devices (such as mobile phones, laptops, etc.), electric vehicles (such as pure electric vehicles, hybrid electric vehicles, plug-in hybrid electric vehicles, electric bicycles, electric scooters, and electric golf carts). , electric trucks, etc.), electric trains, ships and satellites, energy storage systems, etc., but are not limited to these.
  • a secondary battery, a battery module or a battery pack can be selected according to its usage requirements.
  • FIG. 6 is an electrical device as an example.
  • the electric device is a pure electric vehicle, a hybrid electric vehicle, a plug-in hybrid electric vehicle, etc.
  • a battery pack or battery module can be used.
  • the device may be a mobile phone, a tablet, a laptop, etc.
  • the device is usually required to be thin and light, and a secondary battery can be used as a power source.
  • the preparation of the high-nickel ternary cathode material is generally based on Example 1-1. The difference is that in step S1, manganese sulfate is replaced by aluminum sulfate; in step S3, a high-nickel ternary cathode material matrix is obtained, and its molecular formula is: LiNi 0.92 Co 0.06 Mg 0.001 Y 0.002 Al 0.017 O 2 .
  • S3 Put lithium hydroxide and the dried high-nickel ternary precursor into a high mixer according to a Li/Me molar ratio of 1.01, mix at 550rpm for 0.5h, and then put the mixed material into the kiln for sintering.
  • the sintering temperature is 800°C
  • the sintering time is 20h
  • the sintering atmosphere is O 2 .
  • the furnace is cooled to obtain a high-nickel ternary cathode material LiNi 0.92 Co 0.06 Mn 0.02 O 2 .
  • the preparation of the high-nickel ternary cathode material is generally based on Example 1-1. The difference is that no magnesium salt solution is added.
  • step S3 a high-nickel ternary cathode material matrix is obtained, and its molecular formula is LiNi 0.92 Co 0.06 Y 0.002 Mn. 0.018 O 2 .
  • the preparation of the high-nickel ternary cathode material is generally based on Example 1-1. The difference is that the yttrium salt solution is not added.
  • step S3 a high-nickel ternary cathode material matrix is obtained, and its molecular formula is LiNi 0.92 Co 0.06 Mg 0.001 Mn. 0.019 O 2 .
  • the preparation of the high-nickel ternary cathode material is generally as described in Example 1-1, except that in step S4, the amount of cobalt boride is 1000 ppm.
  • the preparation of the high-nickel ternary cathode material is generally as described in Example 1-1, except that in step S4, the amount of cobalt boride is 10,000 ppm.
  • the preparation of the high-nickel ternary cathode material is generally as described in Example 1-1, except that in step S4, the amount of cobalt boride is 15,000 ppm.
  • the preparation of the high-nickel ternary cathode material is generally as described in Example 1-1, except that in step S4, the amount of cobalt boride is 500 ppm.
  • the preparation of the high-nickel ternary cathode material is generally as described in Example 1-1, except that in step S4, the amount of cobalt boride is 16,000 ppm.
  • the preparation of the high-nickel ternary cathode material is generally as described in Example 1-1, except that in step S4, the sintering temperature is 300°C.
  • the preparation of the high-nickel ternary cathode material is generally as described in Example 1-1, except that in step S4, the sintering temperature is 650°C.
  • the preparation of the high-nickel ternary cathode material is generally as described in Example 1-1, except that in step S4, the sintering temperature is 200°C.
  • the preparation of the high-nickel ternary cathode material is generally as described in Example 1-1, except that in step S4, the sintering temperature is 700°C.
  • the preparation of the high-nickel ternary cathode material is generally as described in Example 1-1, except that in step S4, the sintering time is 3 hours.
  • the preparation of the high-nickel ternary cathode material is generally as described in Example 1-1, except that in step S4, the sintering time is 7 hours.
  • the preparation of the high-nickel ternary cathode material is generally as described in Example 1-1, except that in step S4, the sintering time is 2 hours.
  • the preparation of the high-nickel ternary cathode material is generally as described in Example 1-1, except that in step S4, the sintering time is 11 hours.
  • the preparation of the high-nickel ternary cathode material is generally as described in Example 1-1, except that in step S4, the particle size of cobalt boride is 500 nm.
  • the preparation of the high-nickel ternary cathode material is generally as described in Example 1-1, except that in step S4, the particle size of cobalt boride is 2000 nm.
  • the preparation of the high-nickel ternary cathode material is generally as described in Example 1-1, except that in step S4, the particle size of cobalt boride is 3200 nm.
  • the preparation of the high-nickel ternary cathode material is generally as described in Example 1-1, except that in step S4, cobalt boride is replaced by titanium boride.
  • the preparation of the high-nickel ternary cathode material is generally as described in Example 1-1, except that in step S4, the particle size of cobalt boride is 3300 nm.
  • the preparation of the high-nickel ternary cathode material is generally based on Example 1-1, except that in step S4, the sintering atmosphere is oxygen, the sintering temperature is 650°C, and the sintering time is 7 hours.
  • a plasma optical emission spectrometer (ICP-OES) was used, and the equipment model was ICAP7400 from Thermo Fisher Scientific Company of the United States. First, weigh 1g of the sample into a beaker, add 25ml of HNO 3 solution with a concentration of 25% by volume to the sample to dissolve the sample, and dilute it with 475ml of deionized water. Then put the diluted liquid into the instrument for target element analysis. Calculate the target element content.
  • the test method for volume distribution particle size is: refer to GB/T 19077-2016/ISO 13320:2009 particle size distribution laser diffraction method, and the equipment uses Malvern 3000. Take a clean beaker, add an appropriate amount of the sample to be tested to a shading degree of 8%-12%, add 20ml of deionized water, and ultrasonic for 5 minutes, then turn on the particle size tester to start testing.
  • the test method for the specific surface area BET of the ternary precursor is: refer to GB/T 19587-2017 "Determination of the specific surface area of solid materials by gas adsorption BET method", and the equipment uses TriStar II 3020. Take a crystallized special sample tube, use a sampling spoon to add the test sample into the sample tube, and add the amount to 2/3 of the bulb. After taking it, wipe the outside of the tube clean with dust-free paper; then put the sample tube into the tube. Go to the equipment degassing station, degas the sample tube, and finally put the sample into the analysis station for sample analysis.
  • the high-nickel ternary cathode material prepared in the above examples and comparative examples was used as the cathode active material, and was mixed with the conductive agent acetylene black and the binder polyvinylidene fluoride (PVDF) in a weight ratio of 94:3:3 in N- After the mixture is fully stirred and evenly mixed in the methylpyrrolidone solvent system, it is coated on aluminum foil, dried, and cold pressed to obtain a positive electrode piece.
  • PVDF polyvinylidene fluoride
  • Comparing Examples 1-1 to 1-8 and Comparative Examples 1-1 to 1-5 when 0 ⁇ c ⁇ 0.005 and 0 ⁇ d ⁇ 0.01, the 45°C cycle capacity retention rate and the cycle capacity retention rate of the secondary battery can be significantly improved. Storage capacity retention rate at 60°C and degree of material cracking after cycling. Since excessive doping of Mg element or Y element will reduce the energy density of the secondary battery and thus affect the capacity of the secondary battery, 0 ⁇ c ⁇ 0.003 and 0 ⁇ d ⁇ 0.005 are preferred.
  • Example 1-1 and Examples 2-1 to 2-5 shows that as the coating amount of the boron-containing alloy increases, the 45°C cycle capacity retention rate and the 60°C storage capacity retention rate of the battery increase, and the material cracks after cycling. The degree is reduced; however, if the coating amount of boron-containing alloy is too high, the energy density of the secondary battery will be reduced, thereby reducing the capacity of the secondary battery. Therefore, when the coating amount of the boron-containing alloy is preferably 1000-15000 ppm, it can further improve the battery's 45°C cycle capacity retention rate and 60°C storage capacity retention rate, as well as the degree of material cracking after cycling, while also affecting the secondary battery capacity. smaller.
  • Example 1-1 and Examples 3-1 to 3-4 shows that when the sintering temperature in step S4 is 300-650°C, the 45°C cycle capacity retention rate and 60°C storage capacity retention rate of the secondary battery increase and The degree of material cracking after cycling was good.
  • Comprehensive comparison of Example 1-1 and Examples 4-1 to 4-4 shows that when the sintering time of step S4 is 3h-10h, the 45°C cycle capacity retention rate and 60°C storage capacity retention rate of the secondary battery increase as well as cycle The degree of cracking of the final material was good.
  • Example 1-1 and Examples 5-1 to 5-5 shows that when the particle size of the boron-containing alloy is 50-3200nm, the 45°C cycle capacity retention rate and 60°C storage capacity retention rate of the secondary battery can be significantly improved. and the degree of material cracking after cycling.
  • a comprehensive comparison of Example 1-1 and Example 5-6 shows that step S4 of the preparation method of the present application is compatible with two schemes: low-temperature inert atmosphere sintering and high-temperature oxygen atmosphere sintering, including high-nickel trioxide prepared by these two schemes.
  • the secondary battery made of Yuan cathode material has a high cycle capacity retention rate at 45°C and a storage capacity retention rate at 60°C, and at the same time, the degree of material cracking after cycling is low.

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Abstract

本申请涉及一种高镍三元正极材料，包含基体Li 1+xNi aCo bMg cY dM (1-a-b-c-d)O 2±y，M选自Mn、Zr、Al、B、Ta、Mo、W、Nb、Sb、La中的至少一种，其中：0.8≤a＜1.0，0＜b＜0.2，0＜c≤0.005，0＜d≤0.01，a+b+c+d＜1，-0.5＜x＜0.5，0≤y＜0.02，所述基体的表面设置有包覆层，所述包覆层包含含硼合金。本申请还涉及一种制备高镍三元正极材料的方法，以及二次电池、电池模块、电池包和用电装置。

Description

高镍三元正极材料及其制备方法、二次电池、电池模块、电池包和用电装置 技术领域
本申请涉及锂电池技术领域，尤其涉及一种高镍三元正极材料及其制备方法、二次电池、电池模块、电池包和用电装置。
背景技术
近年来，随着锂离子二次电池的应用范围越来越广泛，锂离子二次电池广泛应用于水力、火力、风力和太阳能电站等储能电源系统，以及电动工具、电动自行车、电动摩托车、电动汽车、军事装备、航空航天等多个领域。
由于锂离子二次电池取得了极大的发展，因此对其能量密度、循环性能和安全性能等也提出了更高的要求。而高镍正极活性材料被认为是满足高能量密度要求的最佳选择。但是随着镍含量的不断提高，其结构稳定性越来越差，进而影响锂离子二次电池的循环性能和存储性能。
因此，存在提高锂离子二次电池循环性能和存储性能的需求。
发明内容
本申请是鉴于上述课题而进行的，其目的在于，提供一种高镍三元正极材料，旨在使由其制备的锂离子二次电池在高温下具有良好的循环性能和存储稳定性。
为了达到上述目的，本申请提供了一种高镍三元正极材料及其制备方法、二次电池、电池模块、电池包和用电装置。
本申请的第一方面提供了一种高镍三元正极材料，包含
基体Li 1+xNi aCo bMg cY dM (1-a-b-c-d)O 2±y，M选自Mn、Zr、Al、B、Ta、Mo、W、Nb、Sb、La中的至少一种，其中：0.8≤a＜1.0，0＜b＜0.2， 0＜c≤0.005，0＜d≤0.01，a+b+c+d＜1，-0.5＜x＜0.5，0≤y＜0.02，基体的表面设置有包覆层，包覆层包含含硼合金。
由此，本申请通过将Y元素与Mg元素均匀地分布在材料粉体的外层颗粒中，Y元素有助于形成外层径向棒状颗粒，帮助提升应力变化的各项同性，Mg元素有助于缓和H2-H3相变的剧烈程度，抑制深度充放电过程中的晶胞体积剧烈变化，从而抑制晶内与晶间裂纹的扩展；同时晶界处覆盖的含硼合金既能够吸收晶界处累计的应力疲劳又可以保护活性表面不受电解液副产物的腐蚀，从而改善二次电池在高温下的循环性能与存储稳定性。
在任意实施方式中，含硼合金为M’B z，其中M’选自Co、Ti、Zr、W、Al和Mo中的至少一种，并且0＜z≤4。当含硼合金的z在所给范围内时，有助于提升被包覆后高镍三元正极材料的电子电导率，从而进一步提高高镍三元正极材料的倍率性能。
在任意实施方式中，0＜c≤0.003。当c在所给范围内时，有助于提升高镍三元正极材料的在晶胞体积剧烈变化下的结构稳定性同时又不会过多地影响克容量发挥。
在任意实施方式中，0＜d≤0.005。当d在所给范围内时，有助于提升高镍三元正极材料的颗粒排列有序度与径向分布并抑制晶内裂纹同时又不会导致表层颗粒的比表面积过大而引发过多地副反应。
在任意实施方式中，含硼合金的包覆量为1000ppm-15000ppm，以含硼合金中的金属元素相对于基体的总重量计。当含硼合金的包覆量在所给范围内时，既可以最大化地提升晶界的强度又不会因为堵塞孔隙而造成容量发挥下降。
在任意实施方式中，高镍三元正极材料的粒径Dv 50为3μm-18μm，可选为9μm-14μm，体积分布径距(Dv 90-Dv 10)/Dv 50≥1.30。当高镍三元正极材料的体积分布径距在所给范围内时，能够提高烧结后的高镍三元正极材料的压实密度，从而进一步提高三元正极材料的体积能量密度。
在任意实施方式中，高镍三元正极材料的BET为0.2m 2/g-1m 2/g， 可选为0.3m 2/g-0.7m 2/g。当高镍三元正极材料的BET在所给范围内时，能够减少电解液的腐蚀，从而改善二次电池的存储性能。
在任意实施方式中，高镍三元正极材料的振实密度TD为1.8g/cm 3-2.5g/cm 3，可选为1.9g/cm 3-2.3g/cm 3。当高镍三元正极材料的振实密度TD在所给范围内时，能够改善高镍三元正极材料的加工性能。
本申请的第二方面还提供一种制备高镍三元正极材料的方法，包括以下步骤：
S1：制备Ni、Co和M的混合金属盐溶液，以及镁盐溶液和钇盐溶液；
S2：在反应釜中加入水作为底液，加入碱溶液和氨水调节底液的pH值及氨浓度，将所述Ni、Co和M的混合金属盐溶液、碱溶液、氨水加入至所述反应釜中，维持pH值及氨浓度不变并通入惰性气体进行保护，得到高镍三元前驱体，停止加入所述Ni、Co和M的混合金属盐溶液，将所述镁盐溶液、钇盐溶液、碱溶液、氨水加入至所述反应釜中，维持pH值及氨浓度不变，得到表面掺杂有Mg元素和Y元素的高镍三元前驱体；
S3：将含锂化合物和所述表面掺杂有Mg元素和Y元素的高镍三元前驱体混合并烧结，得到高镍三元正极材料基体；
S4：将所述高镍三元正极材料基体与含硼合金在惰性气氛或空气中混合，然后在惰性气氛或O 2中烧结，得到高镍三元正极材料，
高镍三元正极材料包含
基体Li 1+xNi aCo bMg cY dM (1-a-b-c-d)O 2±y，M选自Mn、Zr、Al、B、Ta、Mo、W、Nb、Sb、La中的至少一种，其中：0.8≤a＜1.0，0＜b＜0.2，0＜c≤0.005，0＜d≤0.01，a+b+c+d＜1，-0.5＜x＜0.5，0≤y＜0.02，基体的表面设置有包覆层，包覆层包含含硼合金。
由此，本申请方法通过在前驱体层级进行掺杂，可以得到具备径向分布结构的前驱体与外层颗粒富含Y和Mg元素的高镍三元正极材料。本申请的方法在步骤S2中有成核与核生长两个过程，能在核上 合成出径向分布的壳层结构，能明显改善烧结后的高镍三元正极材料的长期性能。此外，本申请方法在步骤S4中分为在低温惰性气氛烧结与高温通氧气氛烧结两种方案，前者可以最大化实现含硼合金的优点，后者可以实现合金与残余锂反应并稳定表面的晶格氧。
在任意实施方式中，在步骤S4中，惰性气氛为纯度为99.9％以上的氮气(N 2)或氩气(Ar 2)。
在任意实施方式中，在步骤S4中，烧结的温度为300℃-650℃。
在任意实施方式中，在步骤S4中，烧结的时间为3h-10h。
在任意实施方式中，在步骤S4中，含硼合金的粒度为50nm-3200nm。
本申请的第三方面提供一种二次电池，包括本申请第一方面的高镍三元正极材料或根据本申请第二方面的方法制备的高镍三元正极材料。
本申请的第四方面提供一种电池模块，包括本申请第三方面的二次电池。
本申请的第五方面提供一种电池包，包括本申请第四方面的电池模块。
本申请的第六方面提供一种用电装置，包括选自本申请的第三方面的二次电池、本申请的第四方面的电池模块或本申请的第五方面的电池包中的至少一种。
本申请的电池模块、电池包和用电装置包括本申请的二次电池，因而至少具有与所述二次电池相同的优势。
附图说明
图1是本申请一实施方式的二次电池的示意图。
图2是图1所示的本申请一实施方式的二次电池的分解图。
图3是本申请一实施方式的电池模块的示意图。
图4是本申请一实施方式的电池包的示意图。
图5是图4所示的本申请一实施方式的电池包的分解图。
图6是本申请一实施方式的二次电池用作电源的用电装置的示意图。
附图标记说明：
1电池包；2上箱体；3下箱体；4电池模块；5二次电池；51壳体；52电极组件；53顶盖组件
具体实施方式
以下，适当地参照附图详细说明具体公开了本申请的高镍三元正极材料及其制备方法、二次电池、电池模块、电池包和用电装置的实施方式。但是会有省略不必要的详细说明的情况。例如，有省略对已众所周知的事项的详细说明、实际相同结构的重复说明的情况。这是为了避免以下的说明不必要地变得冗长，便于本领域技术人员的理解。此外，附图及以下说明是为了本领域技术人员充分理解本申请而提供的，并不旨在限定权利要求书所记载的主题。
本申请所公开的“范围”以下限和上限的形式来限定，给定范围是通过选定一个下限和一个上限进行限定的，选定的下限和上限限定了特别范围的边界。这种方式进行限定的范围可以是包括端值或不包括端值的，并且可以进行任意地组合，即任何下限可以与任何上限组合形成一个范围。例如，如果针对特定参数列出了60-120和80-110的范围，理解为60-110和80-120的范围也是预料到的。此外，如果列出的最小范围值1和2，和如果列出了最大范围值3，4和5，则下面的范围可全部预料到：1-3、1-4、1-5、2-3、2-4和2-5。在本申请中，除非有其他说明，数值范围“a-b”表示a到b之间的任意实数组合的缩略表示，其中a和b都是实数。例如数值范围“0-5”表示本文中已经全部列出了“0-5”之间的全部实数，“0-5”只是这些数值组合的缩略表示。另外，当表述某个参数为≥2的整数，则相当于公开了该参数为例如整数2、3、4、5、6、7、8、9、10、11、12等。
如果没有特别的说明，本申请的所有实施方式以及可选实施方式可以相互组合形成新的技术方案。
如果没有特别的说明，本申请的所有技术特征以及可选技术特征 可以相互组合形成新的技术方案。
如果没有特别的说明，本申请的所有步骤可以顺序进行，也可以随机进行，优选是顺序进行的。例如，所述方法包括步骤(a)和(b)，表示所述方法可包括顺序进行的步骤(a)和(b)，也可以包括顺序进行的步骤(b)和(a)。例如，提到所述方法还可包括步骤(c)，表示步骤(c)可以任意顺序加入到所述方法，例如，所述方法可以包括步骤(a)、(b)和(c)，也可包括步骤(a)、(c)和(b)，也可以包括步骤(c)、(a)和(b)等。
如果没有特别的说明，本申请所提到的“包括”和“包含”表示开放式，也可以是封闭式。例如，所述“包括”和“包含”可以表示还可以包括或包含没有列出的其他组分，也可以仅包括或包含列出的组分。
如果没有特别的说明，在本申请中，术语“或”是包括性的。举例来说，短语“A或B”表示“A，B，或A和B两者”。更具体地，以下任一条件均满足条件“A或B”：A为真(或存在)并且B为假(或不存在)；A为假(或不存在)而B为真(或存在)；或A和B都为真(或存在)。
[高镍三元正极材料]
本申请的一个实施方式中，本申请提出了一种高镍三元正极材料，包含
基体Li 1+xNi aCo bMg cY dM (1-a-b-c-d)O 2±y，M选自Mn、Zr、Al、B、Ta、Mo、W、Nb、Sb、La中的至少一种，其中，0.8≤a＜1.0，0＜b＜0.2，0＜c≤0.005，0＜d≤0.01，a+b+c+d＜1，-0.5＜x＜0.5，0≤y＜0.02，基体的表面设置有包覆层，包覆层包含含硼合金。
虽然机理尚不明确，但本申请人意外地发现：本申请通过将Y元素与Mg元素均匀地分布在材料粉体的外层颗粒中，Y元素在外层颗粒的富集可以沉积在垂直于(001)的晶面上，从而导致(001)晶面的生长，使得外层颗粒沿着径向演化为长宽比较大的细长棒状，显著提升了堆叠有序度与各向同性，降低了形变层错率，有利于循环过 程中晶粒体积变化的同频，降低了颗粒间的应力相互作用，抑制晶间裂纹的扩展；Mg元素能够在高镍三元正极材料大量脱嵌锂的过程中提供支柱作用，抑制晶胞体积的剧烈变化，降低H2-H3相变的程度，抑制应力应变效应，从而抑制晶内裂纹的扩展；同时晶界处覆盖的含硼合金在充放电过程中可以很好地吸收晶界处的应力集中，提高晶界的韧性强度，又可以保护活性材料表面不受电解液副产物的腐蚀，抑制高活性材料表面的副反应发生。因此，晶界的强化与均匀包覆可以显著提升高镍三元正极材料的高温循环性能与结构稳定性，从而改善二次电池在高温下与充放电过程的循环性能与存储稳定性。
在一些实施方式中，含硼合金为M’B z，其中M’选自Co、Ti、Zr、W、Al和Mo中的至少一种，并且0＜z≤4。当含硼合金的z在所给范围内时，有助于提升被包覆后高镍三元正极材料的电子电导率，从而进一步提高高镍三元正极材料的倍率性能。
在一些实施方式中，0＜c≤0.003，例如0.0005≤c≤0.003，0.001≤c≤0.003，0.0005≤c≤0.001。当c在所给范围内时，有助于提升高镍三元正极材料的在晶胞体积剧烈变化下的结构稳定性同时又不会过多地影响克容量发挥。
在一些实施方式中，0＜d≤0.005，例如0.001≤d≤0.005，0.002≤d≤0.005。当d在所给范围内时，有助于提升高镍三元正极材料的颗粒排列有序度与径向分布并抑制晶内裂纹同时又不会导致表层颗粒的比表面积过大而引发过多地副反应。
在一些实施方式中，含硼合金的包覆量为1000ppm-15000ppm，以含硼合金中的金属元素相对于基体的总重量计。当含硼合金的包覆量在所给范围内时，既可以最大化地提升晶界的强度又不会因为堵塞孔隙而造成容量发挥下降。
在一些实施方式中，高镍三元正极材料的粒径Dv 50为3μm-18μm，可选为9μm-14μm，体积分布径距(Dv 90-Dv 10)/Dv 50≥1.30。当高镍三元正极材料的体积分布径距在所给范围内时，能够提升烧结后的高镍三元正极材料的压实密度，从而进一步提高高镍三元正极材料的体积 能量密度。
本申请中，高镍三元正极材料的颗粒体积分布粒度Dv 10、Dv 50、Dv 90为本领域的公知概念。具体地，Dv 10为粉体颗粒以体积为基准的粒度分布中，从小粒径侧起、达到体积累计10％的粒径，单位通常为μm。Dv 50为粉体颗粒以体积为基准的粒度分布中，从小粒径侧起、达到体积累计50％的粒径。Dv 90为粉体颗粒以体积为基准的粒度分布中，从小粒径侧起、达到体积累计90％的粒径。上述三元前驱体的颗粒体积分布粒度Dv 10、Dv 50、Dv 90的测试方法可以采用本领域公知的方法进行测试。作为示例，可以参考GB/T 19077-2016/ISO 13320：2009粒度分布激光衍射法，采用设备马尔文3000进行测定。
在一些实施方式中，高镍三元正极材料的BET为0.2m 2/g-1m 2/g，可选为0.3m 2/g-0.7m 2/g。当高镍三元正极材料的BET在所给范围内时，能够减少电解液的腐蚀，从而改善二次电池的存储性能。
本申请中，高镍三元正极材料的比表面积BET的测试方法可以采用本领域公知的方法进行测试。作为示例，可以参考GB/T 19587-2017《气体吸附BET法测定固态物质比表面积》，采用设备TriStar II 3020进行测定。
在一些实施方式中，高镍三元正极材料的振实密度TD为1.8g/cm 3-2.5g/cm 3，可选为1.9g/cm 3-2.3g/cm 3。当高镍三元正极材料的振实密度TD在所给范围内时，能够改善高镍三元正极材料的加工性能。
本申请中，高镍三元正极材料的振实密度TD的测试方法可以采用本领域公知的方法进行测试。作为示例，可以参考GB/T 5162-2006《金属粉末振实密度的测定》，采用设备丹东百特BT-300型号振实密度仪进行测定。
本申请中，在高镍三元正极材料中，Y元素在粉体外层颗粒表面富集导致其沿着径向演化，使得其外层一次颗粒长宽比增加，一次粒子长宽比为3-9。
本申请的一个实施方式中，本申请提出了一种制备高镍三元正极 材料的方法，包括以下步骤：
S1：制备Ni、Co和M的混合金属盐溶液，以及镁盐溶液和钇盐溶液；
S2：在反应釜中加入水作为底液，加入碱溶液和氨水调节底液的pH值及氨浓度，将所述Ni、Co和M的混合金属盐溶液、碱溶液、氨水加入至所述反应釜中，维持pH值及氨浓度不变并通入惰性气体进行保护，得到高镍三元前驱体，停止加入所述Ni、Co和M的混合金属盐溶液，将所述镁盐溶液、钇盐溶液、碱溶液、氨水加入至所述反应釜中，维持pH值及氨浓度不变，得到表面掺杂有Mg元素和Y元素的高镍三元前驱体；
S3：将含锂化合物和所述表面掺杂有Mg元素和Y元素的高镍三元前驱体混合并烧结，得到高镍三元正极材料基体；
S4：将所述高镍三元正极材料基体与含硼合金在惰性气氛或空气中混合，然后在惰性气氛或O 2中烧结，得到高镍三元正极材料，
高镍三元正极材料包含
基体Li 1+xNi aCo bMg cY dM (1-a-b-c-d)O 2±y，M选自Mn、Zr、Al、B、Ta、Mo、W、Nb、Sb、La中的至少一种，其中：0.8≤a＜1.0，0＜b＜0.2，0＜c≤0.005，0＜d≤0.01，a+b+c+d＜1，-0.5＜x＜0.5，0≤y＜0.02，基体的表面设置有包覆层，包覆层包含含硼合金。
由此，本申请的方法通过在前驱体层级进行掺杂，可以避免在烧结时因为杂原子的离子半径等原因迁移至Li层从而达不到TM层支柱的作用；可以得到具备径向分布结构的前驱体与外层颗粒富含Y和Mg元素的高镍三元正极材料。本申请的方法在步骤S2中有成核与核生长两个过程，能在核上合成出径向分布的壳层结构，能明显改善烧结后的高镍三元正极材料的长期性能。此外，本申请方法在步骤S4中分为在低温惰性气氛烧结与高温通氧气氛烧结两种方案，前者可以形成均匀的含硼合金包覆层，进一步强化晶界的韧性，后者可以实现合金与残余锂反应并稳定表面的晶格氧。
在本申请实施例中，在步骤S1中，使用镍盐、钴盐、含M化合 物和纯水制备Ni、Co和M的混合金属盐溶液。对镍盐、钴盐和含M化合物的种类没有特别的限制，可以根据实际需求进行选择。例如，镍盐包括硫酸镍、硝酸镍、乙酸镍中的一种或多种；钴盐包括硫酸钴、草酸钴、硝酸钴、乙酸钴中的一种或多种；当M为锰时，含锰化合物包括硫酸锰、硝酸锰、乙酸锰中的一种或多种；当M为锆时，含锆化合物包括二氧化锆、锆酸锂、氯化锆中的一种或多种；当M为铝时，含铝化合物包括三氧化二铝、氢氧化铝、铝酸锂中的一种或多种；当M为硼时，含硼化合物包括三氧化二硼、硼酸、硼酸锂、硼化锆、硼化钨中的一种或多种；当M为钽时，含钽化合物包括五氧化二钽、氢氧化钽、钽酸锂、氯化钽、氟化钽中的一种或多种；当M为钼时，含钼化合物包括二氧化钼、三氧化钼、钼酸钠、钼酸锂、钼酸酐、氯化钼中的一种或多种；当M为钨时，含钨化合物包括三氧化钨、钨酸钠、钨酸锂、钨酸铵中的一种或多种；当M为铌时，含铌化合物包括五氧化二铌、三氧化二铌、氟化铌、氯化铌、铌酸锂中的一种或多种；当M为锑时，含锑化合物包括三氧化二锑、五氧化二锑、氟代锑酸锂中的一种或多种；当M为镧时，含镧化合物包括三氧化二镧、氯化镧、锆酸镧锂中的一种或多种
在一些实施方式中，在步骤S1中，Ni、Co和M的混合金属盐溶液的浓度为1-5mol/L。
在本申请实施例中，在步骤S1中，对钇盐和镁盐的种类没有特别的限制，可以根据实际需求进行选择。例如，钇盐包括硫酸钇、硝酸钇、草酸钇、乙酸钇、氯化钇中的一种或多种。镁盐包括硫酸镁、硝酸镁、草酸镁、乙酸镁、氯化镁中的一种或多种。
在一些实施方式中，在步骤S1中，钇盐溶液和镁盐溶液的浓度为1-5mol/L。
在一些实施方式中，在步骤S2中，碱溶液例如为氢氧化钠溶液，浓度为1-10mol/L；pH值为9.5-10.5；氨水溶液的浓度为1-5mol/L；氨浓度为0.5-1mol/L，可选为0.65-0.75mol/L；反应温度为65-85℃；搅拌速率为150rpm-350rpm。
在一些实施方式中，在步骤S2中，惰性气体包括高纯(＞99.9％)氮气与氩气。
通过控制步骤S2的工艺条件，可以连续稳定得到平均体积分布粒径Dv 50为3μm-18μm的高镍三元前驱体。通过控制氨浓度与反应温度，有利于形成一次晶粒堆叠良好、层错率较低的高镍三元前驱体晶体结构。通过控制搅拌速率，能够合成颗粒致密、孔隙率均匀的高镍三元前驱体，同时避免大颗粒破碎。
在本申请实施例中，在步骤S3中，对含锂化合物的种类没有具有特别的限制，可根据实际需求进行选择。例如，含锂化合物可以为氢氧化锂、碳酸锂、硝酸锂。
在一些实施方式中，在步骤S3中，含锂化合物中的锂与三元前驱体中镍、钴、M三者之和的摩尔比为(0.9-1.1)∶1。
在一些实施方式中，在步骤S3中，烧结温度为700-900℃；烧结时间为10h-20h；烧结气氛为空气或氧气。
在一些实施方式中，在步骤S4中，惰性气氛为纯度为99.9％以上的氮气(N 2)或氩气(Ar 2)。
在一些实施方式中，在步骤S4中，烧结的温度为300℃-650℃。
在一些实施方式中，在步骤S4中，烧结的时间为3h-10h。
在一些实施方式中，在步骤S4中，含硼合金的粒度为50nm-3200nm。
另外，以下适当参照附图对本申请的二次电池、电池模块、电池包和用电装置进行说明。
本申请的一个实施方式中，提供一种二次电池。
通常情况下，二次电池包括正极极片、负极极片、电解质和隔离膜。在电池充放电过程中，活性离子在正极极片和负极极片之间往返嵌入和脱出。电解质在正极极片和负极极片之间起到传导离子的作用。隔离膜设置在正极极片和负极极片之间，主要起到防止正负极短路的作用，同时可以使离子通过。
[正极极片]
正极极片包括正极集流体以及设置在正极集流体至少一个表面的正极膜层，所述正极膜层包括本申请第一方面的高镍三元正极材料。
作为示例，正极集流体具有在其自身厚度方向相对的两个表面，正极膜层设置在正极集流体相对的两个表面的其中任意一者或两者上。
在一些实施方式中，所述正极集流体可采用金属箔片或复合集流体。例如，作为金属箔片，可采用铝箔。复合集流体可包括高分子材料基层和形成于高分子材料基层至少一个表面上的金属层。复合集流体可通过将金属材料(铝、铝合金、镍、镍合金、钛、钛合金、银及银合金等)形成在高分子材料基材(如聚丙烯(PP)、聚对苯二甲酸乙二醇酯(PET)、聚对苯二甲酸丁二醇酯(PBT)、聚苯乙烯(PS)、聚乙烯(PE)等的基材)上而形成。
在一些实施方式中，正极膜层还可选地包括粘结剂。作为示例，所述粘结剂可以包括聚偏氟乙烯(PVDF)、聚四氟乙烯(PTFE)、偏氟乙烯-四氟乙烯-丙烯三元共聚物、偏氟乙烯-六氟丙烯-四氟乙烯三元共聚物、四氟乙烯-六氟丙烯共聚物及含氟丙烯酸酯树脂中的至少一种。
在一些实施方式中，正极膜层还可选地包括导电剂。作为示例，所述导电剂可以包括超导碳、乙炔黑、炭黑、科琴黑、碳点、碳纳米管、石墨烯及碳纳米纤维中的至少一种。
在一些实施方式中，可以通过以下方式制备正极极片：将上述用于制备正极极片的组分，例如正极活性材料、导电剂、粘结剂和任意其他的组分分散于溶剂(例如N-甲基吡咯烷酮)中，形成正极浆料；将正极浆料涂覆在正极集流体上，经烘干、冷压等工序后，即可得到正极极片。
[负极极片]
负极极片包括负极集流体以及设置在负极集流体至少一个表面上的负极膜层，所述负极膜层包括负极活性材料。
作为示例，负极集流体具有在其自身厚度方向相对的两个表面，负极膜层设置在负极集流体相对的两个表面中的任意一者或两者上。
在一些实施方式中，所述负极集流体可采用金属箔片或复合集流体。例如，作为金属箔片，可以采用铜箔。复合集流体可包括高分子材料基层和形成于高分子材料基材至少一个表面上的金属层。复合集流体可通过将金属材料(铜、铜合金、镍、镍合金、钛、钛合金、银及银合金等)形成在高分子材料基材(如聚丙烯(PP)、聚对苯二甲酸乙二醇酯(PET)、聚对苯二甲酸丁二醇酯(PBT)、聚苯乙烯(PS)、聚乙烯(PE)等的基材)上而形成。
在一些实施方式中，负极活性材料可采用本领域公知的用于电池的负极活性材料。作为示例，负极活性材料可包括以下材料中的至少一种：人造石墨、天然石墨、软炭、硬炭、硅基材料、锡基材料和钛酸锂等。所述硅基材料可选自单质硅、硅氧化合物、硅碳复合物、硅氮复合物以及硅合金中的至少一种。所述锡基材料可选自单质锡、锡氧化合物以及锡合金中的至少一种。但本申请并不限定于这些材料，还可以使用其他可被用作电池负极活性材料的传统材料。这些负极活性材料可以仅单独使用一种，也可以将两种以上组合使用。
在一些实施方式中，负极膜层还可选地包括粘结剂。所述粘结剂可选自丁苯橡胶(SBR)、聚丙烯酸(PAA)、聚丙烯酸钠(PAAS)、聚丙烯酰胺(PAM)、聚乙烯醇(PVA)、海藻酸钠(SA)、聚甲基丙烯酸(PMAA)及羧甲基壳聚糖(CMCS)中的至少一种。
在一些实施方式中，负极膜层还可选地包括导电剂。导电剂可选自超导碳、乙炔黑、炭黑、科琴黑、碳点、碳纳米管、石墨烯及碳纳米纤维中的至少一种。
在一些实施方式中，负极膜层还可选地包括其他助剂，例如增稠剂(如羧甲基纤维素钠(CMC-Na))等。
在一些实施方式中，可以通过以下方式制备负极极片：将上述用于制备负极极片的组分，例如负极活性材料、导电剂、粘结剂和任意其他组分分散于溶剂(例如去离子水)中，形成负极浆料；将负极浆 料涂覆在负极集流体上，经烘干、冷压等工序后，即可得到负极极片。
[电解质]
电解质在正极极片和负极极片之间起到传导离子的作用。本申请对电解质的种类没有具体的限制，可根据需求进行选择。例如，电解质可以是液态的、凝胶态的或全固态的。
在一些实施方式中，所述电解质采用电解液。所述电解液包括电解质盐和溶剂。
在一些实施方式中，电解质盐可选自六氟磷酸锂、四氟硼酸锂、高氯酸锂、六氟砷酸锂、双氟磺酰亚胺锂、双三氟甲磺酰亚胺锂、三氟甲磺酸锂、二氟磷酸锂、二氟草酸硼酸锂、二草酸硼酸锂、二氟二草酸磷酸锂及四氟草酸磷酸锂中的至少一种。
在一些实施方式中，溶剂可选自碳酸亚乙酯、碳酸亚丙酯、碳酸甲乙酯、碳酸二乙酯、碳酸二甲酯、碳酸二丙酯、碳酸甲丙酯、碳酸乙丙酯、碳酸亚丁酯、氟代碳酸亚乙酯、甲酸甲酯、乙酸甲酯、乙酸乙酯、乙酸丙酯、丙酸甲酯、丙酸乙酯、丙酸丙酯、丁酸甲酯、丁酸乙酯、1，4-丁内酯、环丁砜、二甲砜、甲乙砜及二乙砜中的至少一种。
在一些实施方式中，所述电解液还可选地包括添加剂。例如添加剂可以包括负极成膜添加剂、正极成膜添加剂，还可以包括能够改善电池某些性能的添加剂，例如改善电池过充性能的添加剂、改善电池高温或低温性能的添加剂等。
[隔离膜]
在一些实施方式中，二次电池中还包括隔离膜。本申请对隔离膜的种类没有特别的限制，可以选用任意公知的具有良好的化学稳定性和机械稳定性的多孔结构隔离膜。
在一些实施方式中，隔离膜的材质可选自玻璃纤维、无纺布、聚乙烯、聚丙烯及聚偏二氟乙烯中的至少一种。隔离膜可以是单层薄膜，也可以是多层复合薄膜，没有特别限制。在隔离膜为多层复合薄膜时，各层的材料可以相同或不同，没有特别限制。
在一些实施方式中，正极极片、负极极片和隔离膜可通过卷绕工 艺或叠片工艺制成电极组件。
在一些实施方式中，二次电池可包括外包装。该外包装可用于封装上述电极组件及电解质。
在一些实施方式中，二次电池的外包装可以是硬壳，例如硬塑料壳、铝壳、钢壳等。二次电池的外包装也可以是软包，例如袋式软包。软包的材质可以是塑料，作为塑料，可列举出聚丙烯、聚对苯二甲酸丁二醇酯以及聚丁二酸丁二醇酯等。
本申请对二次电池的形状没有特别的限制，其可以是圆柱形、方形或其他任意的形状。例如，图1是作为一个示例的方形结构的二次电池5。
在一些实施方式中，参照图2，外包装可包括壳体51和盖板53。其中，壳体51可包括底板和连接于底板上的侧板，底板和侧板围合形成容纳腔。壳体51具有与容纳腔连通的开口，盖板53能够盖设于所述开口，以封闭所述容纳腔。正极极片、负极极片和隔离膜可经卷绕工艺或叠片工艺形成电极组件52。电极组件52封装于所述容纳腔内。电解液浸润于电极组件52中。二次电池5所含电极组件52的数量可以为一个或多个，本领域技术人员可根据具体实际需求进行选择。
在一些实施方式中，二次电池可以组装成电池模块，电池模块所含二次电池的数量可以为一个或多个，具体数量本领域技术人员可根据电池模块的应用和容量进行选择。
图3是作为一个示例的电池模块4。参照图3，在电池模块4中，多个二次电池5可以是沿电池模块4的长度方向依次排列设置。当然，也可以按照其他任意的方式进行排布。进一步可以通过紧固件将该多个二次电池5进行固定。
可选地，电池模块4还可以包括具有容纳空间的外壳，多个二次电池5容纳于该容纳空间。
在一些实施方式中，上述电池模块还可以组装成电池包，电池包所含电池模块的数量可以为一个或多个，具体数量本领域技术人员可根据电池包的应用和容量进行选择。
图4和图5是作为一个示例的电池包1。参照图4和图5，在电池包1中可以包括电池箱和设置于电池箱中的多个电池模块4。电池箱包括上箱体2和下箱体3，上箱体2能够盖设于下箱体3，并形成用于容纳电池模块4的封闭空间。多个电池模块4可以按照任意的方式排布于电池箱中。
另外，本申请还提供一种用电装置，所述用电装置包括本申请提供的二次电池、电池模块、或电池包中的至少一种。所述二次电池、电池模块、或电池包可以用作所述用电装置的电源，也可以用作所述用电装置的能量存储单元。所述用电装置可以包括移动设备(例如手机、笔记本电脑等)、电动车辆(例如纯电动车、混合动力电动车、插电式混合动力电动车、电动自行车、电动踏板车、电动高尔夫球车、电动卡车等)、电气列车、船舶及卫星、储能系统等，但不限于此。
作为所述用电装置，可以根据其使用需求来选择二次电池、电池模块或电池包。
图6是作为一个示例的用电装置。该用电装置为纯电动车、混合动力电动车、或插电式混合动力电动车等。为了满足该用电装置对二次电池的高功率和高能量密度的需求，可以采用电池包或电池模块。
作为另一个示例的装置可以是手机、平板电脑、笔记本电脑等。该装置通常要求轻薄化，可以采用二次电池作为电源。
实施例
以下，说明本申请的实施例。下面描述的实施例是示例性的，仅用于解释本申请，而不能理解为对本申请的限制。实施例中未注明具体技术或条件的，按照本领域内的文献所描述的技术或条件或者按照产品说明书进行。所用试剂或仪器未注明生产厂商者，均为可以通过市购获得的常规产品。
实施例1-1
S1：使用硫酸镍、硫酸钴、硫酸锰和纯水按摩尔比Ni∶Co∶Mn＝92∶6∶2配置浓度为2mol/L的镍钴锰混合金属盐溶液，使用 硫酸钇按摩尔比Y∶Me＝0.2％∶1配置浓度为4mol/L的钇盐溶液，使用硫酸镁按摩尔比Mg∶Me＝0.1％∶1配置浓度为4mol/L的镁盐溶液，其中Me为镍、钴、锰的摩尔数之和；
S2：在50L的反应釜中加入25L去离子水作为底液，加入4mol/L的氨水溶液调整底液氨浓度为0.75mol/L，加入5mol/L的NaOH溶液调整底液pH值为10.0；在氮气气氛下，将底液加热至75℃，在250rpm搅拌转速下，将镍钴锰混合金属盐溶液、NaOH溶液、氨水溶液并流加入底液中，维持反应釜中pH值及氨浓度不变，当Dv 50达到7.5μm时，停止加入镍钴锰混合金属盐溶液，将钇盐溶液和镁盐溶液、NaOH溶液、氨水溶液并流加入反应釜中，维持反应釜中pH值及氨浓度不变，直至合成得到Dv 50＝9μm的高镍三元前驱体，陈化3h，将获得的高镍三元前驱体进行洗涤，离心，干燥；
S3：将氢氧化锂和干燥后的高镍三元前驱体按照Li/Me摩尔比为1.03放入高混机中，在550rpm下混合0.5h，然后将混合物料放入窑炉中进行烧结，烧结温度为760℃，烧结时间为20h，烧结气氛为O 2，烧结后随炉冷却即得到高镍三元正极材料基体，其分子式为LiNi 0.92Co 0.06Mg 0.001Y 0.002Mn 0.017O 2；
S4：将高镍三元正极材料基体与粒度为50nm的硼化钴放入高混机中，在N 2气氛下，在400rpm下混合0.4h，其中硼化钴的量为5000ppm，再将混合物放入窑炉中进行烧结，烧结温度为350℃，烧结时间为10h，烧结气氛为N 2，烧结完成后进行液氮快速降温至常温的淬火处理，即得到高镍三元正极材料。
实施例1-2
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S1中，采用硫酸镁按摩尔比Mg∶Me＝0.05％∶1配置浓度为4mol/L的镁盐溶液；在步骤S3中，得到高镍三元正极材料基体，其分子式为LiNi 0.92Co 0.06Mg 0.0005Y 0.002Mn 0.0175O 2。
实施例1-3
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在 步骤S1中，采用硫酸镁按摩尔比Mg∶Me＝0.3％∶1配置浓度为4mol/L的镁盐溶液；在步骤S3中，得到高镍三元正极材料基体，其分子式为LiNi 0.92Co 0.06Mg 0.003Y 0.002Mn 0.015O 2。
实施例1-4
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S1中，采用硫酸镁按摩尔比Mg∶Me＝0.5％∶1配置浓度为4mol/L的镁盐溶液；在步骤S3中，得到高镍三元正极材料基体，其分子式为LiNi 0.92Co 0.06Mg 0.005Y 0.002Mn 0.013O 2。
实施例1-5
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S1中，采用硫酸钇按摩尔比Y∶Me＝0.1％∶1配置浓度为4mol/L的钇盐溶液；在步骤S3中，得到高镍三元正极材料基体，其分子式为LiNi 0.92Co 0.06Mg 0.001Y 0.001Mn 0.018O 2。
实施例1-6
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S1中，采用硫酸钇按摩尔比Y∶Me＝0.5％∶1配置浓度为4mol/L的钇盐溶液；在步骤S3中，得到高镍三元正极材料基体，其分子式为LiNi 0.92Co 0.06Mg 0.001Y 0.005Mn 0.014O 2。
实施例1-7
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S1中，采用硫酸钇按摩尔比Y∶Me＝1％∶1配置浓度为4mol/L的钇盐溶液；在步骤S3中，得到高镍三元正极材料基体，其分子式为LiNi 0.92Co 0.06Mg 0.001Y 0.01Mn 0.009O 2。
实施例1-8
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S1中，将硫酸锰替换为硫酸铝；在步骤S3中，得到高镍三元正极材料基体，其分子式为LiNi 0.92Co 0.06Mg 0.001Y 0.002Al 0.017O 2。
对比例1-1
S1：使用硫酸镍、硫酸钴、硫酸锰和纯水按摩尔比 Ni∶Co∶Mn＝92∶6∶2配置浓度为2mol/L的镍钴锰混合金属盐溶液；
S2：在50L反应釜中加入25L去离子水作为底液，加入4mol/L的氨水溶液调整底液氨浓度为0.75mol/L，加入5mol/L的NaOH溶液调整底液pH值为10.0；在氮气气氛下，将底液加热至75℃，在250rpm搅拌转速下，将镍钴锰混合金属盐溶液、NaOH溶液、氨水溶液并流加入底液中，维持反应釜中pH值及氨浓度不变，直至合成得到Dv 50＝9μm的高镍三元前驱体，陈化3h，将获得的高镍三元前驱体进行洗涤，离心，干燥；
S3：将氢氧化锂和干燥后的高镍三元前驱体按照Li/Me摩尔比为1.01放入高混机中，在550rpm下混合0.5h，然后将混合物料放入窑炉中进行烧结，烧结温度为800℃，烧结时间为20h，烧结气氛为O 2，烧结后随炉冷却得到高镍三元正极材料LiNi 0.92Co 0.06Mn 0.02O 2。
对比例1-2
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，不加入镁盐溶液，在步骤S3中，得到高镍三元正极材料基体，其分子式为LiNi 0.92Co 0.06Y 0.002Mn 0.018O 2。
对比例1-3
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，不加入钇盐溶液，在步骤S3中，得到高镍三元正极材料基体，其分子式为LiNi 0.92Co 0.06Mg 0.001Mn 0.019O 2。
对比例1-4
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S1中，采用硫酸镁按摩尔比Mg∶Me＝0.6％∶1配置浓度为4mol/L的镁盐溶液；在步骤S2中，不加入钇盐溶液；在步骤S3中，得到高镍三元正极材料基体，其分子式为LiNi 0.92Co 0.06Mg 0.006Mn 0.014O 2。
对比例1-5
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S1中，采用硫酸钇按摩尔比Y∶Me＝1.5％∶1配置浓度为4mol/L的钇盐溶液；在步骤S2中，不加入镁盐溶液；在步骤S3中，得到高 镍三元正极材料基体，其分子式为LiNi 0.92Co 0.06Y 0.015Mn 0.005O 2。
实施例2-1
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S4中，硼化钴的量为1000ppm。
实施例2-2
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S4中，硼化钴的量为10000ppm。
实施例2-3
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S4中，硼化钴的量为15000ppm。
实施例2-4
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S4中，硼化钴的量为500ppm。
实施例2-5
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S4中，硼化钴的量为16000ppm。
实施例3-1
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S4中，烧结温度为300℃。
实施例3-2
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S4中，烧结温度为650℃。
实施例3-3
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S4中，烧结温度为200℃。
实施例3-4
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S4中，烧结温度为700℃。
实施例4-1
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S4中，烧结时间为3h。
实施例4-2
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S4中，烧结时间为7h。
实施例4-3
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S4中，烧结时间为2h。
实施例4-4
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S4中，烧结时间为11h。
实施例5-1
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S4中，硼化钴的粒度为500nm。
实施例5-2
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S4中，硼化钴的粒度为2000nm。
实施例5-3
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S4中，硼化钴的粒度为3200nm。
实施例5-4
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S4中，将硼化钴替换为硼化钛。
实施例5-5
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S4中，硼化钴的粒度为3300nm。
实施例5-6
高镍三元正极材料的制备整体上参照实施例1-1，区别在于，在步骤S4中，烧结气氛为氧气，烧结温度为650℃，烧结时间为7h。
测试方法
1.高镍三元正极材料基体的测定
采用等离子体发射光谱仪(ICP-OES)，设备型号为美国Thermo Fisher Scientific公司ICAP7400。首先称取1g样品于烧杯中，向样品中加入25ml浓度为25％体积比的HNO 3溶液将样品溶解，并用475ml去离子水进行稀释，然后将稀释液体放入仪器设备进行目标元素分析，经计算得到目标元素含量。
2.体积分布粒度
体积分布粒度的测试方法为：参考GB/T 19077-2016/ISO 13320：2009粒度分布激光衍射法，设备采用马尔文3000。取洁净烧杯，加入待测样品适量至遮光度8％-12％，加入20ml去离子水，同时外超声5min，开启粒度测试仪开始测试。
3.比表面积BET
三元前驱体的比表面积BET的测试方法为：参考GB/T 19587-2017《气体吸附BET法测定固态物质比表面积》，设备采用TriStar II 3020。取一根结晶的专用样品管，用取样勺将测试样品加入至样品管中，加入量在球泡的2/3处，取完后用无尘纸将管外擦拭干净；然后将样品管装到设备脱气站上，对样品管进行脱气处理，最后将样品放入分析站中进行样品分析。
4.振实密度TD
三元前驱体的振实密度TD的测试方法为：参考GB/T 5162-2006《金属粉末振实密度的测定》，设备为振实密度仪。先称量干净干燥的100ml量筒重量为m 0g，再装入一定量的粉末样品，称量总重为m 1g，将装有粉料的量筒放入振实密度仪上，开启设备，设置振动次数为5000次，振完后读取体积为V cm 3，振实密度＝(m 1-m 0)/V，单位为g/cm 3。
5.循环后材料开裂程度
利用图像法输出颗粒开裂的百分比：将在45℃下循环500圈之 后的电池极片取出后通过离子抛光获得平整断面，通过扫描电子显微镜(Scanning Electron Microscope，简称SEM)观察样品颗粒分布并选定灰度差异明显的、分辨率高的目标颗粒，用imageJ软件通过调整阈值获得单颗粒开裂部分所占百分比，收集30个颗粒的信息并求取平均值，该数值即为此样品的循环后材料开裂程度。
6.制备全电池：
将上述各实施例和对比例中制备的高镍三元正极材料作为正极活性材料，与导电剂乙炔黑、粘结剂聚偏二氟乙烯(PVDF)按重量比94∶3∶3在N-甲基吡咯烷酮溶剂体系中充分搅拌混合均匀后，涂覆于铝箔上烘干、冷压，得到正极极片。将负极活性物质人造石墨、硬碳，导电剂乙炔黑，粘结剂丁苯橡胶(SBR)，增稠剂碳甲基纤维素钠(CMC)按照重量比90∶5∶2∶2∶1在去离子水溶剂体系中充分搅拌混合均匀后，涂覆于铜箔上烘干、冷压，得到负极极片。以聚乙烯多孔聚合薄膜作为隔离膜。将正极极片、隔离膜、负极极片按顺序叠好，使隔离膜处于正负极片中间起到隔离的作用，并卷绕得到裸电芯。将裸电芯置于外包装中，注入配好的基础电解液，即1mol/L的LiPF 6/(EC+EMC+DMC)(体积比为1∶1∶1)，并封装，得到全电池。
全电初始克容量测试方法：
在25℃恒温环境下，静置5min，按照1/3C放电至2.8V，静置5min，按照1/3C充电至4.25V，然后在4.25V下恒压充电至电流≤0.05mA，静置5min，此时的充电容量记为C 0，然后按照1/3C放电至2.8V，此时的放电容量为初始克容量，记为D 0。
45℃循环容量性能测试：
在45℃的恒温环境下，在2.8-4.25V下，按照1C充电至4.25V，然后在4.25V下恒压充电至电流≤0.05mA，静置5min，然后按照1C放电至2.8V，容量记为D 0，重复前面过程，记录容量D n(n＝0，1，2......)，计算500次循环容量保持率：D 500/D 0*100％。
60℃存储容量保持率：
在25℃的恒温环境下，进行完整的克容量测试(参考《全电初 始克容量测试方法》)，容量记为D 0，然后将电池由0.33C恒流充电至4.25V并恒压至电流≤0.05mA，静置5min，然后放入60℃的高低温箱中，静置1h待电池温度达到目标温度后进行存储。15天后取出，在25℃的恒温环境下，重复前面过程，并每隔15天记录一次容量D n(n＝0，1，2......)，计算105天存储后容量保持率：D 7/D 0*100％。
按照上述过程分别测试上述实施例和对比例，具体数值参见表1-表5。
Figure PCTCN2022081676-appb-000001
Figure PCTCN2022081676-appb-000002
Figure PCTCN2022081676-appb-000003
Figure PCTCN2022081676-appb-000004
Figure PCTCN2022081676-appb-000005
Figure PCTCN2022081676-appb-000006
由表1至表5可知，上述所有实施例的二次电池的45℃循环容量保持率和60℃存储容量保持率均高于对比例的二次电池。此外，所有实施例的二次电池的循环后材料开裂程度显著降低。这说明通过将Y元素与Mg元素均匀地分布在材料粉体的外层颗粒中并对颗粒进行包覆，可以明显改善二次电池的45℃循环容量保持率、60℃存储容量保持率和循环后材料开裂程度。
综合比较实施例1-1至1-8和对比例1-1至1-5，当0＜c≤0.005，0＜d≤0.01时，能够明显改善二次电池的45℃循环容量保持率、60℃存储容量保持率和循环后材料开裂程度。由于Mg元素或者Y元素掺杂量过多会降低二次电池的能量密度，从而影响二次电池的容量，因此优选0＜c≤0.003，0＜d≤0.005。
综合比较实施例1-1和实施例2-1至2-5，随着含硼合金的包覆量增加，电池的45℃循环容量保持率和60℃存储容量保持率增加，循环后材料开裂程度降低；但是，如果含硼合金的包覆量太高，会降低二次电池的能量密度，进而降低二次电池的容量。因此，优选含硼合金的包覆量为1000-15000ppm时，能够进一步改善电池的45℃循环容量保持率和60℃存储容量保持率增加以及循环后材料开裂程度，同时对二次电池容量的影响较小。
综合比较实施例1-1和实施例3-1至3-4，当步骤S4的烧结温度为300-650℃时，二次电池的45℃循环容量保持率和60℃存储容量保持率增加以及循环后材料开裂程度均良好。综合比较实施例1-1和实施例4-1至4-4，当步骤S4的烧结时间为3h-10h时，二次电池的45℃循环容量保持率和60℃存储容量保持率增加以及循环后材料开裂程度均良好。
综合比较实施例1-1和实施例5-1至5-5，当含硼合金的粒度为50-3200nm时，能明显改善二次电池的45℃循环容量保持率、60℃存储容量保持率和循环后材料开裂程度。此外，综合比较实施例1-1和实施例5-6，本申请制备方法的步骤S4能够兼容低温惰性气氛烧结与高温通氧气氛烧结两种方案，包含由这两种方案制备的高镍三元正 极材料的二次电池具有较高的45℃循环容量保持率和60℃存储容量保持率，同时循环后材料开裂程度较低。
需要说明的是，本申请不限定于上述实施方式。上述实施方式仅为示例，在本申请的技术方案范围内具有与技术思想实质相同的构成、发挥相同作用效果的实施方式均包含在本申请的技术范围内。此外，在不脱离本申请主旨的范围内，对实施方式施加本领域技术人员能够想到的各种变形、将实施方式中的一部分构成要素加以组合而构筑的其它方式也包含在本申请的范围内。

Claims (17)

  1. 一种高镍三元正极材料，包含
    基体Li 1+xNi aCo bMg cY dM (1-a-b-c-d)O 2±y，M选自Mn、Zr、Al、B、Ta、Mo、W、Nb、Sb、La中的至少一种，其中：0.8≤a＜1.0，0＜b＜0.2，0＜c≤0.005，0＜d≤0.01，a+b+c+d＜1，-0.5＜x＜0.5，0≤y＜0.02，所述基体的表面设置有包覆层，所述包覆层包含含硼合金。
  2. 根据权利要求1所述的高镍三元正极材料，其特征在于，所述含硼合金为M’B z，其中M’选自Co、Ti、Zr、W、Al和Mo中的至少一种，并且0＜z≤4。
  3. 根据权利要求1或2所述的高镍三元正极材料，其特征在于，0＜c≤0.003。
  4. 根据权利要求1至3中任一项所述的高镍三元正极材料，其特征在于，0＜d≤0.005。
  5. 根据权利要求1至4中任一项所述的高镍三元正极材料，其特征在于，所述含硼合金的包覆量为1000ppm-15000ppm，以所述含硼合金中的金属元素相对于基体的总重量计。
  6. 根据权利要求1至5中任一项所述的高镍三元正极材料，其特征在于，所述高镍三元正极材料的粒径Dv 50为3μm-18μm，可选为9μm-14μm，体积分布径距(Dv 90-Dv 10)/Dv 50≥1.30。
  7. 根据权利要求1至6中任一项所述的高镍三元正极材料，其特征在于，所述高镍三元正极材料的BET为0.2m 2/g-1m 2/g，可选为0.3m 2/g-0.7m 2/g。
  8. 根据权利要求1至7中任一项所述的高镍三元正极材料，其特征在于，所述高镍三元正极材料的振实密度TD为1.8g/cm 3-2.5g/cm 3，可选为1.9g/cm 3-2.3g/cm 3。
  9. 一种制备高镍三元正极材料的方法，包括以下步骤：
    S1：制备Ni、Co和M的混合金属盐溶液，以及镁盐溶液和钇盐溶液；
    S2：在反应釜中加入水作为底液，加入碱溶液和氨水调节底液的pH值及氨浓度，将所述Ni、Co和M的混合金属盐溶液、碱溶液、氨水加入至所述反应釜中，维持pH值及氨浓度不变并通入惰性气体进行保护，得到高镍三元前驱体，停止加入所述Ni、Co和M的混合金属盐溶液，将所述镁盐溶液、钇盐溶液、碱溶液、氨水加入至所述反应釜中，维持pH值及氨浓度不变，得到表面掺杂有Mg元素和Y元素的高镍三元前驱体；
    S3：将含锂化合物和所述表面掺杂有Mg元素和Y元素的高镍三元前驱体混合并烧结，得到高镍三元正极材料基体；
    S4：将所述高镍三元正极材料基体与含硼合金在惰性气氛或空气中混合，然后在惰性气氛或O 2中烧结，得到高镍三元正极材料；
    其中，所述高镍三元正极材料包含：
    基体Li 1+xNi aCo bMg cY dM (1-a-b-c-d)O 2±y，M选自Mn、Zr、Al、B、Ta、Mo、W、Nb、Sb、La中的至少一种，其中：0.8≤a＜1.0，0＜b＜0.2，0＜c≤0.005，0＜d≤0.01，a+b+c+d＜1，-0.5＜x＜0.5，0≤y＜0.02，所述基体的表面设置有包覆层，所述包覆层包含含硼合金。
  10. 根据权利要求9所述的方法，其特征在于，在步骤S4中，所述惰性气氛为纯度为99.9％以上的氮气(N 2)或氩气(Ar 2)。
  11. 根据权利要求9或10所述的方法，其特征在于，在步骤S4 中，所述烧结的温度为300℃-650℃。
  12. 根据权利要求9至11中任一项所述的方法，其特征在于，在步骤S4中，所述烧结的时间为3h-10h。
  13. 根据权利要求9至12中任一项所述的方法，其特征在于，在步骤S4中，所述含硼合金的粒度为50nm-3200nm。
  14. 一种二次电池，其特征在于，包括权利要求1至8中任一项所述的高镍三元正极材料或通过权利要求9至13中任一项所述的方法制备的高镍三元正极材料。
  15. 一种电池模块，其特征在于，包括权利要求14所述的二次电池。
  16. 一种电池包，其特征在于，包括权利要求15所述的电池模块。
  17. 一种用电装置，其特征在于，包括选自权利要求14所述的二次电池、权利要求15所述的电池模块或权利要求16所述的电池包中的至少一种。
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EP22902462.5A EP4276945A1 (en) 2022-03-18 2022-03-18 High-nickel ternary positive electrode material and preparation method therefor, secondary battery, battery module, battery pack, and electrical device

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