Patent Application
20250233154
The present application claims priority to Chinese Patent Application No. 202310093288.0, entitled “LITHIUM-ION BATTERY AND ELECTRICAL DEVICE”, and filed to the China National Intellectual Property Administration on Feb. 10, 2023, the entire contents of which are incorporated herein by reference.
The present application relates to the field of lithium-ion batteries, and in particular relates to a lithium-ion battery and an electrical device.
In recent years, with the development of new energy vehicles, lithium-ion batteries have been widely used due to their advantages such as high voltage, high energy density, long cycle life, low self-discharge, and non-pollution. Lithium-ion batteries are the power source of new energy vehicles, and their properties of charging speed, cycle life, and safety are crucial for lithium-ion batteries. The lithium-ion battery includes a positive electrode plate and a negative electrode plate relatively arranged, a separator separating the positive electrode plate and the negative electrode plate, and an electrolyte between the positive electrode plate and the negative electrode plate. The positive electrode plate includes a positive current collector and a positive electrode coating arranged on at least one surface of the positive current collector, and the negative electrode plate includes a negative current collector and a negative electrode coating arranged on at least one surface of the negative current collector. When a lithium-ion battery is charged, lithium-ions are deintercalated from the positive electrode active material, migrated to the negative electrode plate through the electrolyte under the action of an electric field, and are intercalated in the negative electrode active material.
The imbalance between a rate of deintercalation of lithium ions from the positive electrode active material and a rate of intercalation of lithium ions into the negative electrode active material limits the charging capacity of lithium-ion batteries.
Therefore, the present application provides a lithium-ion battery and an electrical device to solve the technical problem of how to improve the charging capacity of the lithium-ion battery.
The first aspect of the present application provides a lithium-ion battery, including a positive electrode plate and a negative electrode plate. The positive electrode plate includes a positive current collector and a positive electrode coating arranged on at least one surface of the positive current collector. The negative electrode plate includes a negative current collector and a negative electrode coating arranged on at least one surface of the negative current collector. A lithium ion migration kinetic coefficient Fc of the positive electrode coating and A lithium ion migration kinetic coefficient Fa of the negative electrode coating satisfy: 0.25≤Fc/Fa≤5; Fc=2 (Dvc50+5Mc)+PDc/4Pc, where Dvc50 μm is an average particle size of a positive active material in the positive electrode coating; McΩ is the internal resistance of the positive electrode plate; PDc g/cm3 is a compaction density of the positive electrode coating; Pc is a porosity of the positive electrode coating; Fa=Dva50+Ma+PDa/2Pa, where Dva50 μm is an average particle size of a negative active material in the negative electrode coating; Ma mΩ is an internal resistance of the negative electrode plate; PDa g/cm3 is a compaction density of the negative electrode coating; Pa is a porosity of the negative electrode coating.
Optionally, the lithium ion migration kinetic coefficient Fc of the positive electrode coating and the lithium ion migration kinetic coefficient Fa of the negative electrode coating satisfy: 0.25≤Fc/Fa≤2.8.
Optionally, the lithium ion migration kinetic coefficient Fc of the positive electrode coating is in a range from 6 to 33, and the lithium ion migration kinetic coefficient Fa of the negative electrode coating is in a range from 7 to 40.
Optionally, the lithium ion migration kinetic coefficient Fc of the positive electrode coating is in a range from 8 to 22, and the lithium ion migration kinetic coefficient Fa of the negative electrode coating is in a range from 10 to 28.
Optionally, the average particle size of the positive electrode active material is in a range from 2 μm to 8 μm, the internal resistance of the positive electrode plate is in a range from 0.05Ω to 1.6Ω, the compaction density of the positive electrode coating is in a range from 3.0 g/cm3 to 3.8 g/cm3, and the porosity of the positive electrode coating is in a range from 20% to 50%; and the average particle size of the negative active material is in a range from 6 μm to 20 μm, the internal resistance of the negative electrode plate is in a range from 0.8 mΩ to 15 mΩ, the compaction density of the negative electrode coating is in a range from 1.4 g/cm3 to 1.8 g/cm3, and the porosity of the negative electrode coating is in a range from 20% to 60%.
Optionally, the average particle size of the positive electrode active material is in a range from 2.53 μm to 7.56 μm, the internal resistance of the positive electrode plate is in a range from 0.05Ω to 0.9Ω, the compaction density of the positive electrode coating is in a range from 3.1 g/cm3 to 3.6 g/cm3, and the porosity of the positive electrode coating is in a range from 20% to 40%; and the average particle size of the negative active material is 8 μm to 18 μm, the internal resistance of the negative electrode plate is in a range from 0.8 mΩ to 10 mΩ, the compaction density of the negative electrode coating is in a range from 1.4 g/cm3 to 1.7 g/cm3, and the porosity of the negative electrode coating is in a range from 35% to 55%.
Optionally, at least some of the positive electrode active materials are single crystal particles.
Optionally, the positive electrode active material includes a modified positive electrode active material.
Optionally, the modified positive electrode active material includes a doping element, and the doping element includes at least one of Al, Zr, Sr, Ti, B, Mg, V, Ba, W, Y and Nb.
Optionally, the modified positive electrode active material includes a coating agent, and the constituent elements of the coating agent include at least one of Li, Al, Ti, Mn0, Zr, Mg, Zn, Ba, Mo, B, W and Co.
Optionally, the coating agent includes metal oxides and/or inorganic salts, wherein the metal oxide includes an oxide formed from at least one of Al, Ti, Mn, Zr, Mg, Zn, Ba, Mo, B, W and Co, and the inorganic salt includes at least one of Li2ZrO3, LiNbO3, Li4Ti5O12, Li2TiO3, LiTiO2, Li3VO4, LiSnO3, Li2SiO3, LiAlO2, AIPO4 and AlF3.
The second aspect of the present application provides an electrical device including the aforementioned lithium-ion battery.
The lithium-ion battery provided in the present application can achieve the following beneficial effects:
The following will provide a clear and complete description of the technical solution of the present application in conjunction with the examples. Obviously, the described examples are a part of the embodiments of the present application, not all of them. Based on the examples in the present application, all other embodiments obtained by ordinary technical personnel in this field without creative labor will fall within the scope of protection in the present application. In addition, the technical features involved in different embodiments of the present application described below can be combined with each other as long as they do not conflict with each other.
This embodiment provides a lithium-ion battery, including a shell, and a positive electrode plate, a negative electrode plate, a separator and an electrolyte which are located within the shell. The positive electrode plate and the negative electrode plate are arranged opposite each other, and the separator is used to separate the positive electrode plate and the negative electrode plate. The positive electrode plate includes a positive current collector and a positive electrode coating arranged on at least one surface of the positive current collector. The negative electrode plate includes a negative current collector and a negative electrode coating arranged on at least one surface of the negative current collector. The lithium ion migration kinetic coefficient Fc of the positive electrode coating and the lithium ion migration kinetic coefficient Fa of the negative electrode coating satisfy:
In the above-mentioned lithium-ion battery, a ratio of the lithium ion migration kinetic coefficient Fc of the positive electrode coating to the lithium ion migration kinetic coefficient Fa of the negative electrode coating is greater than or equal to 0.25 and less than or equal to 5, such that a rate of deintercalation of lithium ions from the positive electrode coating is relatively balanced with a rate of intercalation of lithium ions into the negative electrode coating, and the charging current is not limited by the relatively smaller speed of the deintercalation rate and intercalation rate of lithium ions, thereby improving the charging capacity of lithium-ion batteries. At the same time, the degree of lithium precipitation caused by the imbalance between the deintercalation rate and intercalation rate of lithium ions is weakened, the loss of lithium ions is reduced, the attenuation of battery capacity during the cycling charging and discharging process of lithium-ion batteries is reduced, the cycling performance of batteries is improved, the service life of batteries is extended, and the risk of safety hazards caused by lithium dendrites is reduced. In addition, a battery polarization is avoided, which is beneficial for improving the cycling performance of the batteries and extending the service life of the batteries.
For example, the lower limit value of Fc/Fa can be any one selected from 0.25, 0.26, 0.27, 0.28, 0.29, 0.30, 0.31, 0.32, 0.33, 0.34 and 0.35, and the upper limit value of Fc/Fa can be any one selected from 2.5, 2.8, 3.0, 3.2, 3.4, 3.6, 3.8, 4.0, 4.2, 4.4, 4.6, 4.8 and 5.0, or a range composed of any two values therein.
In some embodiments, the positive electrode coating and the negative electrode coating satisfy 0.25≤F/Fa≤3.8.
In some embodiments, the positive electrode coating and the negative electrode coating satisfy 0.25≤F/Fa≤3.0.
In some embodiments, the positive electrode coating and the negative electrode coating satisfy 0.25≤Fc/Fa≤2.8. The comprehensive performance of lithium-ion batteries can be better improved when Fc/Fa is within the above range.
In some embodiments, the lithium ion migration kinetic coefficient Fc of the positive electrode coating is in a range from 6 to 33, and the lithium ion migration kinetic coefficient Fa of the negative electrode coating is in a range from 7 to 40. By limiting the lithium ion migration kinetic coefficient Fc of the positive electrode coating in a range from 6 to 33, a rate of deintercalation of lithium ions from the positive electrode active material is faster, and by limiting the lithium ion migration kinetic coefficient Fa of the negative electrode coating in a range from 7 to 40, a rate of intercalation of lithium ions into the negative electrode active material is faster, thereby enabling the lithium-ion battery to have a faster charging speed. For example, the lithium ion migration kinetic coefficient Fc of the positive electrode coating may be any value selected from 6, 8, 10, 15, 20, 22, 25, 28, 30 and 33, or a range composed of any two values therein. The lithium ion migration kinetic coefficient Fa of the negative electrode coating may be any value selected from 7, 10, 15, 20, 25, 28, 30, 35 and 40, or a range composed of any two values therein.
In some embodiments, the lithium ion migration kinetic coefficient Fc of the positive electrode coating is in a range from 8 to 22, and the lithium ion migration kinetic coefficient Fa of the negative electrode coating is in a range from 10 to 28.
In some embodiments, an average particle size Dvc50 μm of a positive electrode active material is in a range from 2 μm to 8 μm. If the average particle size of the positive electrode active material is too large, it will lead to a too large transmission distance of lithium ions, thereby affecting the deintercalation rate of lithium ions. If the average particle size of the positive electrode active material is too small, it will produce more side reactions with the electrolyte, affecting the high-temperature storage and gas production performance of lithium-ion batteries. By adjusting the average particle size Dvc50 μm of the positive electrode active material into the above range, it not only reduces the transmission distance of lithium ions, thereby increasing the deintercalation rate of lithium ions, but also limits the degree of side reactions between the positive electrode active material and the electrolyte, which is beneficial for the high-temperature storage and gas production performance of lithium-ion batteries. For example, the average particle size Dvc50 μm of the positive electrode active material may be any value of 2 μm, 2.53 μm, 3 μm, 4 μm, 5 μm, 6 μm, 7 μm, 7.56 μm and 8 μm, or can be a range composed of any two values therein.
In some embodiments, the average particle size Dvc50 μm of the positive electrode active material is in a range from 2.53 μm to 7.56 μm.
For an average particle size of the positive electrode active material in the positive electrode coating, a positive electrode plate is placed in a muffle furnace, maintained at a high temperature of 400° C. for 4-5 hours, and then the sintered product is separated from the current collector, then the liquid phase is filtered by centrifugation, dried and separated to obtain a sample of the positive electrode active material in the positive electrode coating. In some embodiments, the average particle size Dva50 μm of the negative active material is in a range from 6 μm to 20 μm. If the average particle size of the negative electrode active material is too large, it will lead to a too large transmission distance of lithium ions, thereby affecting the intercalation speed of lithium ions. If the average particle size of the negative electrode active material is too small, it will produce more side reactions with the electrolyte, affecting the high-temperature storage and gas production performance of lithium-ion batteries. By adjusting the average particle size Dva50 μm of the negative electrode active material into the above range, it not only reduces the transmission distance of lithium ions, thereby increasing the deintercalation rate of lithium ions, but also limits the degree of side reactions between negative electrode active materials and electrolyte, which is beneficial for the high-temperature storage and gas production performance of lithium-ion batteries. For example, the average particle size Dva50 μm of negative active material may be any value selected from 6 μm, 8 μm, 10 μm, 12 μm, 14 μm, 16 μm, 18 μm, and 20 μm, or a range composed of any two values therein.
In some embodiments, the average particle size Dva50 μm of the negative active material is in a range from 8 μm to 18 μm.
For the negative active material in the negative electrode coating, a negative electrode plate is soaked in DMC (dimethyl carbonate) solution, cleaned, dried, and then heat-treated at 800° C. under an argon atmosphere for 2 hours. After separating, a sample of the negative active material in the negative electrode coating is obtained.
In some embodiments, an internal resistance McΩ of the positive electrode plate is in a range from 0.05Ω to 1.6Ω. The smaller internal resistance of the positive electrode plate reduces the comprehensive impedance of lithium-ion batteries, allowing for faster migration rate of lithium ions in the positive electrode coating, which is beneficial for improving the charging capacity of lithium-ion batteries. For example, the internal resistance McΩ of the positive electrode plate can be any value of 0.05 Ω, 0.07 Ω, 0.09 Ω, 0.1 Ω, 0.2 Ω, 0.4 Ω, 0.5 Ω, 0.6 Ω, 0.8 Ω, 0.9 Ω, 1.00 Ω, 1.04 Ω, 1.1 Ω, 1.2 Ω, 1.4 Ω, 1.6Ω, or a range composed of any two values therein.
In some embodiments, the internal resistance McΩ of the positive electrode plate is in a range from 0.05Ω to 0.9 Ω.
In some embodiments, the internal resistance McΩ of the positive electrode plate is in a range from 0.05Ω to 0.5 Ω.
In some embodiments, the internal resistance Ma mΩ of the negative electrode plate is in a range from 0.8 mΩ to 15 mΩ. The smaller internal resistance of negative electrode plate reduces the comprehensive impedance of lithium-ion batteries, allowing for faster migration of lithium ions in the negative electrode coating, which is beneficial for improving the charging capacity of lithium-ion batteries. For example, the internal resistance Ma mΩ of the negative electrode plate can be any value of 0.8 mΩ, 1.0 mΩ, 2.0 mΩ, 3.0 mΩ, 5.0 mΩ, 7.0 mΩ, 8.0 mΩ, 10 mΩ, 12 mΩ, 13 mΩ, 14 mΩ, 15 mΩ, or a range composed of any two values therein.
In some embodiments, the internal resistance Ma mΩ of the negative electrode plate is in a range from 0.8 mΩ to 10 mΩ.
In some embodiments, a compaction density PDc g/cm3 of the positive electrode coating is in a range from 3.0 g/cm3 to 3.8 g/cm3, and a porosity of the positive electrode coating is in a range from 20% to 50%. In general, the smaller the compaction density of the positive electrode coating, the greater the porosity of the positive electrode coating, the more developed the internal pore structure, the better the ability to retain the electrolyte, the better the contact effect between the electrolyte and the positive electrode coating, and the better the liquid phase conductivity ability of lithium ions inside the pores of the positive electrode coating. However, the excessive porosity of the positive electrode coating can lead to too small electron transmission ability, thereby affecting its charging ability. By limiting the compaction density and porosity of the positive electrode coating into the above range, the transmission capacity of lithium ions and electrons is balanced, resulting in excellent transmission capacity of both lithium ions and electrons in the positive electrode coating, which is beneficial for improving the charging capacity of lithium-ion batteries. At the same time, limiting the compaction density and porosity of the positive electrode coating into the above range can ensure that the positive electrode active material has high particle integrity and good electrical contact effect between adjacent particles, which is conducive to improving the energy density of lithium-ion batteries. For example, the compaction density of the positive electrode coating, PDc g/cm3, may be any value of 3.0 g/cm3, 3.1 g/cm3, 3.2 g/cm3, 3.3 g/cm3, 3.4 g/cm3, 3.5 g/cm3, 3.6 g/cm3, 3.7 g/cm3, 3.8 g/cm3, or a range composed of any two values therein. The porosity of the positive electrode coating is any value of 20%, 25%, 30%, 35%, 40%, 45%, 50%, or a range composed of any two values therein.
In some embodiments, the compaction density PDc g/cm3 of the positive electrode coating is in a range from 3.1 g/cm3 to 3.6 g/cm3, and the porosity of the positive electrode coating is in a range from 20% to 40%.
In some embodiments, a compaction density PDa g/cm3 of the negative electrode coating is in a range from 1.4 g/cm3 to 1.8 g/cm3, and a porosity of the negative electrode coating is in a range from 20% to 60%. In general, the smaller the compaction density of the negative electrode coating, the greater the porosity of the negative electrode coating, the more developed the internal pore structure, the better the ability to retain the electrolyte, the better the contact effect between the electrolyte and the negative electrode coating, and the better the liquid phase conductivity ability of lithium ions inside the pores of the negative electrode coating. However, the excessive porosity of the negative electrode coating can lead to too small electron transmission ability, thereby affecting its charging ability. By limiting the compaction density and porosity of the negative electrode coating into the above range, the transmission capacity of lithium ions and electrons is balanced, resulting in excellent transmission capacity of both lithium ions and electrons in the negative electrode coating, which is beneficial for improving the charging capacity of lithium-ion batteries. At the same time, limiting the compaction density and porosity of the negative electrode coating into the above range can ensure that the negative electrode active material has high particle integrity and good electrical contact effect between adjacent particles, which is conducive to improving the energy density of lithium-ion batteries. For example, the compaction density PDa g/cm3 of the negative electrode coating is 1.4 g/cm3, 1.5 g/cm3, 1.6 g/cm3, 1.7 g/cm3 or 1.8 g/cm3. The porosity of the negative electrode coating may be any value selected from 20%, 25%, 30%, 35%, 40%, 45%, 50%, 55%, 60%, or a range composed of any two values therein.
In some embodiments, the compaction density PDa g/cm3 of the negative electrode coating is in a range from 1.4 g/cm3 to 1.7 g/cm3, and the porosity of the negative electrode coating is in a range from 35% to 55%.
It should be understood that the compaction density of the positive electrode coating or the negative electrode coating is defined as PD=m/V, where m represents the weight of the coating and V represents the volume of the coating. m can be measured and obtained using an electronic balance with an accuracy of 0.01 g or more, and the product of the surface area of the coating and the thickness of the coating is the volume V of the coating, where the thickness can be measured and obtained using a spiral micrometer with an accuracy of 0.5 μm. The internal resistance McΩ and Ma mΩ of the positive and negative electrode plates can be tested and obtained using a membrane resistance testing system. The porosity P of the positive and negative electrode coatings can be obtained by gas displacement method, with porosity P=(V1−V2)/V1×100%, wherein V1 represents the apparent volume, V2 represents the actual volume. The measurement step for the average particle size Dv50 of positive and negative active materials is to use a laser diffraction particle size distribution measuring instrument to measure the particle size distribution based on the particle size distribution laser diffraction method (refer to GB/T19077-2016 for details), and the median value of the volume distribution is the value of Dv50.
In some embodiments, the positive electrode active material includes lithium-containing compound with a layered structure, the lithium-containing compound is LiMO2, and M includes at least one of Ni, Co, Al and Mn, such as spinel lithium manganate and spinel lithium nickel manganate.
In some embodiments, the positive electrode active material includes lithium nickel cobalt manganese oxide, with a nickel element content greater than 0.3 and less than 0.85 calculated based on the molar amount of nickel, cobalt and manganese elements being 1.
In some embodiments, the positive electrode active material includes lithium nickel cobalt manganese oxide, with a nickel element content greater than 0.4 and less than 0.85 calculated based on the molar amount of nickel, cobalt and manganese elements being 1.
In some embodiments, the positive electrode active material includes lithium nickel cobalt manganese oxide, with a nickel element content greater than 0.52 and less than 0.83 calculated based on the molar amount of nickel, cobalt and manganese elements being 1.
In some embodiments, the positive electrode active material includes lithium nickel cobalt aluminum oxide, with a nickel element content greater than 0.5 and less than 0.85 calculated based on the molar amount of nickel, cobalt and aluminum elements being 1.
In some embodiments, at least some of the positive electrode active materials are single crystal particles. This can reduce the contact area between the positive electrode active material and the electrolyte, thereby reducing the occurrence of interface side reactions and thereby reducing the gas production amount inside the lithium-ion batteries, which is beneficial for improving the cycling performance of lithium-ion batteries.
In some embodiments, the positive electrode active material is a modified positive electrode active material.
In some embodiments, the modified positive electrode active material includes a doping element, and the doping element includes at least one of Al, Zr, Sr, Ti, B, Mg, V, Ba, W, Y, Nb, F, P and S. By doping in the lattice of the positive electrode active material, the cation mixing of Li/Ni in the positive electrode active material can be inhibited, which helps to reduce the first irreversible capacity, makes the layered structure of the positive electrode active material more complete, makes the crystal structure more stable, and makes the probability of particle breakage and crystal structure damage more lower, which is beneficial for improving the cycling performance and thermal stability of lithium-ion batteries.
In some embodiments, doping agents containing F ions are used. F ions not only promote the sintering of the positive electrode active material and make the structure of the positive electrode active material more stable, but also stabilize the interface between the positive electrode active material and the electrolyte during battery cycling, which is beneficial for improving the cycling performance of lithium-ion batteries. The modification method of ion doping is not limited, which can be modified in the way of wet doping in the precursor co-precipitation stage, or can be modified in the way of dry doping in the sintering stage.
In some embodiments, the modified positive electrode active material includes a coating agent, and the constituent elements of the coating agent include at least one of Li, Al, Ti, Mn, Zr, Mg, Zn, Ba, Mo, B, W and Co. The above coating elements can form a protective layer with better performance on the surface of the positive electrode active material particles, thereby reducing direct contact between the electrolyte and the positive electrode active material, and improving the cycling performance of the battery.
In some embodiments, the coating agent includes metal oxides, wherein the metal oxide includes an oxide formed from at least one of Al, Ti, Mn, Zr, Mg, Zn, Ba, Mo, B, W and Co.
In some embodiments, the coating agent includes inorganic salts, wherein the inorganic salt includes at least one of Li2ZrO3, LiNbO3, Li4Ti3O12, Li2TiO3, LiTiO2, Li3VO4, LiSnO3, Li2SiO3, LiAlO2, AIPO4 and AlF3.
The coating agent forms a coating layer on the surface of the positive electrode active material, which can avoid direct contact between the electrolyte and the positive electrode active material, thereby greatly reducing the side reactions between the electrolyte and the positive electrode active material, reducing the dissolution of transition metals from the positive electrode active material into the electrolyte, and thereby improving the electrochemical stability of the positive electrode active material. The existence of the coating layer can also reduce the degree of crystal structure collapse of the positive electrode active material during repeated charging and discharging processes, reduce the probability of particle breakage and crystal structure damage, and thus improve the cycling performance of lithium-ion batteries. The specific modification method of coating is not limited, which can be modified in the way of wet coating in the precursor co-precipitation stage, or can be modified in the way of dry coating in the sintering stage.
In some embodiments, the negative electrode active material includes at least one of graphite, soft carbon, hard carbon, carbon fibers, mesophase carbon microspheres, silicon-based materials, tin-based materials and lithium titanate. Graphite can be at least one of artificial graphite, natural graphite and modified graphite. Silicon-based materials can be selected from one or more of elemental silicon, oxides of silicon, silicon carbon composites and silicon alloys. The tin-based materials can be selected from one or more of elemental substance tin, tin oxides and tin alloys.
In some embodiments, the positive current collector includes but is not limited to aluminum foil, nickel foil or polymer conductive film, the negative current collector includes but is not limited to copper foil, carbon coated copper foil or polymer conductive film, and the separator includes but is not limited to polyethylene film, polypropylene film, polyvinylidene fluoride film and multi-layer composite film composed of the aforementioned materials.
In some embodiments, the positive current collector is aluminum foil, and the negative current collector is copper foil.
In some embodiments, the positive and negative electrode coatings also include conductive agents and binders. The types and contents of conductive agents and binders are not subject to specific restrictions and can be selected according to actual needs.
In some embodiments, the electrolyte includes lithium salts and organic solvents. The lithium salt includes but is not limited to at least one of lithium hexafluorophosphate, lithium tetrafluoroborate and lithium perchlorate. The organic solvent includes but is not limited to at least one of cyclic carbonates, chain carbonates and carboxylates. The electrolyte can also contain functional additives, such as ethylene carbonate, ethylene sulfate, 1,3-propanesulfonic acid lactone, fluoroethylene carbonate, etc.
The following provides a clear and complete description of the technical solution of the present application by providing specific embodiments as examples. Obviously, the described examples are a part of the embodiments of the present application, not all of them.
The positive electrode active material LiaNixCoyM1-x-yO2 with a Dvc50 μm of 2.5 μm, conductive agent acetylene black, and binder PVDF were mixed in a mass ratio of 96:3:1, solvent NMP was added, and the mixture was stirred with a vacuum mixer until the system was uniform to obtain positive electrode slurry. The positive electrode active material was LiaNixCoyM1-x-yO2, and the molar content of Ni, Co, and Mn met the requirement of Ni:Co:Mn=6:1:3 (hereinafter referred to as NCM613); the positive electrode slurry was uniformly coated on the positive electrode current collector, dried at room temperature, transferred to an oven for further drying, and then cold pressed to achieve a positive electrode coating with the compaction density of 3.2 g/cm3, and cut into positive electrode plates. The internal resistance of the positive electrode plate was 0.282Ω, and the porosity of the positive electrode coating was 25.58%.
The negative electrode active material with a Dva50 μm of 18.5 μm, conductive agent acetylene black, thickener CMC, and binder SBR were mixed in a mass ratio of 96.1:1.0:1.0:1.9, and then the mixture was added with solvent deionized water, and stirred with a vacuum mixer until the system was uniform to obtain negative electrode slurry; the negative electrode slurry was uniformly coated on the negative electrode current collector, dried at room temperature, transferred to an oven for further drying, and then cold pressed twice to achieve a negative electrode coating with compaction density of 1.6 g/cm3, and cut into negative electrode plates, and the internal resistance of the negative electrode plate was 4.81 mΩ, and the porosity of the negative electrode coating was 34.27%.
The preparation scheme of the positive electrode plate described in this example is the same as that in Example 1. The preparation method of the positive electrode plate was the same, with the only difference being that adjusting the cold pressing process, such that the compaction density of the positive electrode coating, the internal resistance of the positive electrode plate, and the porosity of the positive electrode coating were as shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 1. The preparation method of the negative electrode plate was the same, with the only difference being that adjusting the cold pressing process, such that the compaction density of the negative electrode coating was 1.5 g/cm3, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 1. The preparation method of the positive electrode plate was the same, with the only difference being that the average particle size of the positive active material, Dva50 μm, was adjusted to 1.8 μm, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 1.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 3. The preparation method of the positive electrode plate was the same, with the difference being that the average particle size of the positive active material, Dvc50 μm, was adjusted to 3.5 μm, and the internal resistance of the positive electrode plate, the porosity of the positive electrode coating, and the compaction density of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 1. The preparation method of the negative electrode plate was the same, with the differences being that the average particle size of the negative active material, Dva50 μm, was adjusted to 17.5 μm, and the cold pressing process was adjusted to make the compaction density of the negative electrode coating as 1.8 g/cm3, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 4. The preparation method of the positive electrode plate was the same, with the differences being that 100 ppm of tungsten and 200 ppm of strontium were doped in the preparation process of the positive active material; and the cold pressing process was adjusted to make the compaction density of the positive electrode coating as 3.5 g/cm3, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that of Example 4, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 4. The preparation method of the positive electrode plate was the same, with the differences being that adjusting the cold pressing process such that the compaction density of the positive electrode coating was 3.5 g/cm3, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 1. The preparation method of the negative electrode plate was the same, with the differences being that the average particle size of the negative active material, Dva50 μm, was 16.4 μm, the compaction density of the negative electrode coating was 1.8 g/cm3, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 6. The preparation method of the positive electrode plate was the same, with the difference being that the average particle size of the positive active material, Dvc50 in μm was 4.2 μm, adjusting the cold pressing process such that the compaction density of the positive electrode coating was 3.1 g/cm3, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 6. The preparation method of the negative electrode plate was the same, with the differences being that the negative active material, conductive agent acetylene black, thickener CMC, and adhesive SBR were mixed in a mass ratio of 96.5:0.7:1.0:1.8, the compaction density of the negative electrode coating was 1.45 g/cm3, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 7. The preparation method of the positive electrode plate was the same, with the difference being that the cold pressing process was controlled such that the compaction density of the positive electrode coating was 3.2 g/cm3, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 6. The preparation method of the negative electrode plate was the same, with the only difference being that the average particle size of the negative active material Dva50 μm was 14.8 μm, the compaction density of the negative electrode coating was 1.45 g/cm3, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 7. The preparation method of the positive electrode plate was the same, with the only difference being that the cold pressing process was controlled such that the compaction density of the positive electrode coating was 3.3 g/cm3, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 8. The preparation method of the negative electrode plate was the same, with the differences being that the compaction density of the negative electrode coating was 1.6 g/cm3, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 7. The preparation method of the positive electrode plate was the same, with the difference being that the cold pressing process was controlled such that the compaction density of the positive electrode coating was 3.4 g/cm3, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 8. The preparation method of the negative electrode plate was the same, with the difference being that the compaction density of the negative electrode coating was controlled to be 1.75 g/cm3, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 7. The preparation method of the positive electrode plate was the same, with the only difference being that the cold pressing process was controlled such that the compaction density of the positive electrode coating was 3.5 g/cm3, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 6. The preparation method of the negative electrode plate was the same, with the differences being that the average particle size of the negative active material, Dva50 μm, was 13.5 μm, the cold pressing process was controlled such that the compaction density of the negative electrode coating was 1.55 g/cm3, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that of Example 11. The preparation method of the positive electrode plate was the same, with the differences being that the positive active material, conductive agent acetylene black, and binder PVDF were mixed in a mass ratio of 96.5:2.5:1, and the cold pressing process was controlled such that the compaction density of the positive electrode coating was 3.5 g/cm3, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 11. The preparation method of the negative electrode plate is the same, with the difference being that the internal resistance of the negative electrode plate and the porosity of the negative electrode coating are shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that of Example 11. The preparation method of the positive electrode plate was the same, with the difference being that the positive active material, conductive agent acetylene black, and binder PVDF were mixed in a mass ratio of 97.5:1.5:1, and the cold pressing process was controlled such that the compaction density of the positive electrode coating was 3.5 g/cm3, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as Example 11. The preparation method of the negative electrode plate was the same, with the difference being that the compaction density of the negative electrode coating was 1.6 g/cm3, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 11. The preparation method of the positive electrode plate was the same, with the difference being that the positive active material, conductive agent acetylene black, and binder PVDF were mixed in a ratio of 95:4:1, the cold pressing process was controlled such that the compaction density of the positive electrode coating was 3.5 g/cm3, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 13. The preparation method of the negative electrode plate was the same, with the difference being that the mixing time of the negative active material, conductive agent acetylene black, thickener CMC, and adhesive SBR was shortened by 1 hour, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that of Example 10. The preparation method of the positive electrode plate was the same, with the difference being that the average particle size of the positive active material, Dvc50 μm, was 5.8 μm, and the internal resistance of the positive electrode plate, the porosity of the positive electrode coating, and the compaction density of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 13. The preparation method of the negative electrode plate was the same, with the difference being that the average particle size of the negative active material, Dva50 μm, was 7.2 μm, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 15. The preparation method of the positive electrode plate was the same, with the difference being that the cold pressing process was controlled such that the compaction density of the positive electrode coating was 3.5 g/cm3, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 13. The preparation method of the negative electrode plate was the same, with the difference being that the average particle size of the negative active material, Dva50 μm, was 6.3 μm, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 15. The preparation method of the positive electrode plate was the same, with the difference being that the cold pressing process was controlled such that the compaction density of the positive electrode coating was 3.6 g/cm3, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 13. The preparation method of the negative electrode plate was the same, with the difference being that the average particle size of the negative active material, Dva50 μm, was 10.6 μm, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that of Example 16. The preparation method of the positive electrode plate was the same, with the difference being that the average particle size of the positive active material, Dvc50 μm, was 6.4 μm, and the internal resistance of the positive electrode plate, the porosity of the positive electrode coating, and the compaction density of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 17. The preparation method of the negative electrode plate was the same, with the difference being that the negative electrode coating being cold pressed twice becomes being cold pressed once, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 18. The preparation method of the positive electrode plate was the same, with the difference being that the cold pressing process was controlled such that the compaction density of the positive electrode coating was 3.6 g/cm3, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that of Example 18. The preparation method of the negative electrode plate was the same, with the difference being that the mixing time of the negative active material, conductive agent acetylene black, thickener CMC, and adhesive SBR was extended by 1 hour, and the internal resistance of the negative electrode plate, the porosity of the negative electrode coating, and the compaction density of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 18. The preparation method of the positive electrode plate was the same, with the difference being that the cold pressing process was controlled such that the compaction density of the positive electrode coating was 3.7 g/cm3, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that of Example 18. The preparation method of the negative electrode plate was the same, with the difference being that the mixing time of the negative active material, conductive agent acetylene black, thickener CMC, and adhesive SBR was shortened by 1 hour, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 8. The preparation method of the positive electrode plate was the same, with the difference being that the average particle size of the positive active material, Dvc50 μm, was 7.5 μm, and the internal resistance of the positive electrode plate, the porosity of the positive electrode coating, and the compaction density of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 1. The preparation method of the negative electrode plate was the same, with the difference being that the average particle size of the negative active material, Dva50 μm, was 6.0 μm, the cold pressing process was controlled such that the compaction density of the negative electrode coating was 1.6 g/cm3, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that of Example 21. The preparation method of the positive electrode plate was the same, with the difference being that the cold pressing process was controlled such that the compaction density of the positive electrode coating was 3.5 g/cm3, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as Example 21.
The preparation scheme of the positive electrode plate described in this example was the same as that of Example 21. The preparation method of the positive electrode plate was the same, with the difference being that the cold pressing process was controlled such that the compaction density of the positive electrode coating was 3.85 g/cm3, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as Example 21.
The preparation scheme of the positive electrode plate described in this example was the same as that of Example 22. The preparation method of the positive electrode plate was the same, with the difference being that the positive active material, conductive agent acetylene black, and binder PVDF were mixed in a mass ratio of 97:2:1, and the internal resistance of the positive electrode plate, the porosity of the positive electrode coating, and the compaction density of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 23. The preparation method of the negative electrode plate was the same, with the difference being that the average particle size of the negative active material, Dva50 μm, was 12.0 μm, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 9. The preparation method of the positive electrode plate was the same, with the difference being that the positive active material was LiaNixCoyM1-x-yO2, wherein the molar content of Ni, Co, and Mn satisfies Ni:Co:Mn=8:1:1 (hereinafter referred to as NCM811), the Dvc50 μm of the positive active material was 3.9 μm, and the internal resistance of the positive electrode plate, the porosity of the positive electrode coating, and the compaction density of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 23. The preparation method of the negative electrode plate was the same, with the difference being that the average particle size of the negative active material, Dva50 μm, was 6.5 μm, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that of Implementation 25. The preparation method of the positive electrode plate was the same, with the difference being that the cold pressing process was controlled such that the compaction density of the positive electrode coating was 3.5 g/cm3, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode sheet in this example was the same as in Example 25, and the preparation method of the negative electrode sheet was the same.
The preparation scheme of the positive electrode plate described in this example was the same as that of Example 26. The preparation method of the positive electrode plate was the same, with the difference being that the positive active material, conductive agent acetylene black, and binder PVDF were mixed in a mass ratio of 98:1:1, and the internal resistance of the positive electrode plate, the porosity of the positive electrode coating, and the compaction density of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 25. The preparation method of the negative electrode plate was the same, with the difference being that the negative active material, conductive agent acetylene black, thickener CMC, and adhesive SBR were mixed in a mass ratio of 96.0:1.3:1.0:1.7, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 25. The preparation method of the positive electrode plate was the same, with the only difference being that the average particle size of the positive active material, Dvc50 μm, was 4.3 μm, and the internal resistance of the positive electrode plate, the porosity of the positive electrode coating, and the compaction density of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode sheet in this example was the same as in Example 25, and the preparation method of the negative electrode sheet was the same.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 28. The preparation method of the positive electrode plate was the same, with the only difference being that cold pressing causes the compaction density of the positive electrode coating to be 3.6 g/cm3, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 25. The preparation method of the negative electrode plate was the same, with the difference being that the average particle size of the negative active material, Dva50 μm, was 8.5 μm, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 28. The preparation method of the positive electrode plate was the same, with the difference being that the cold pressing process was controlled such that the compaction density of the positive electrode coating was 3.5 g/cm3, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode sheet in this example was the same as in Example 25, and the preparation method of the negative electrode sheet was the same.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 7. The preparation method of the positive electrode plate was the same, with the difference being that the average particle size of the positive active material, Dvc50 μm, was 2.0 μm, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 1. The preparation method of the negative electrode plate was the same, with the difference being that the average particle size of the negative active material, Dva50 μm, was 16.5 μm, cold pressing results in a compaction density of 1.7 g/cm3 for the negative electrode coating, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 20. The preparation method of the positive electrode plate was the same, with the differences being that the average particle size of the positive active material, Dvc50 μm, was 9.0 μm, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 1. The preparation method of the negative electrode plate was the same, with the differences being that the average particle size of the negative active material, Dva50 μm, was 4.0 μm, cold pressing results in a compaction density of 1.5 g/cm3 for the negative electrode coating, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 6. The preparation method of the positive electrode plate was the same, with the differences being that the average particle size of the positive active material, Dvc50 μm, was 2.3 μm, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Example 1. The preparation method of the negative electrode plate was the same, with the differences being that the average particle size of the negative active material, Dva50 μm, was 20.5 μm, cold pressing results in a compaction density of 1.65 g/cm3 for the negative electrode coating, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
The preparation scheme of the positive electrode plate described in this example was the same as that in Example 20. The preparation method of the positive electrode plate was the same, with the differences being that the average particle size of the positive active material, Dvc50 μm, was 10.5 μm, and the internal resistance of the positive electrode plate and the porosity of the positive electrode coating were shown in Table 1.
The preparation scheme of the negative electrode plate described in this example was the same as that in Comparative Example 2. The preparation method of the negative electrode plate was the same, with the differences being that the average particle size of the negative active material, Dva50 μm, was 4.5 μm, and the internal resistance of the negative electrode plate and the porosity of the negative electrode coating were shown in Table 2.
Ethylene carbonate (EC), methyl ethyl carbonate (EMC), and diethyl carbonate (DEC) were mixed in a mass ratio of 1:1:1, then 1 mol/L of LiPF6 was added and mix evenly. Then 1% ethylene carbonate was added to prepare an electrolyte.
A PP separator with thickness of 16 μm was selected as the separator.
The assembly process of lithium-ion batteries included: the positive electrode plate, the separator, and the negative electrode plate were stacked in sequence, so that the separator separates the positive electrode plate and the negative electrode plate, and a stacking structure was obtained; the stacked structure was wound to obtain a bare battery cell; the bare battery cell was placed in the shell, dried and injected with electrolyte. Lithium-ion batteries were obtained through processes such as vacuum packaging, standing, formation, and shaping.
Table 1 showed the materials and parameters of the positive electrode active materials in Examples 1-30 and Comparative Examples 1-4. Table 2 showed the materials and parameters of the negative electrode active materials in Examples 1-30 and Comparative Examples 1-4.
The steps of testing the resistance of the electrode plates included: preparing a test sample with a test area of 154.025 mm2, a triggering pressure of 0.390 t, a sampling time of 15 s, and 10 tests. The average value obtained was the internal resistance of the sample.
The steps of testing the porosity of the coating included: referring to the standard GB/T 21650.2-2008, using the mercury intrusion method and gas adsorption method to determine the pore size distribution and porosity of solid materials; using gas adsorption method for determining the amount of adsorbed gas in mesopores and macropores; and measuring the porosity of the coating using the static capacity method.
The F/Fa of the lithium-ion batteries provided by the Examples and Comparative Examples were calculated, and the dynamic performance and cycling performance tests were performed on the lithium-ion batteries provided by the Examples and Comparative Examples. The results were shown in Table 3.
Among them, the steps of testing the dynamic performance include: at 25° C., the lithium-ion batteries provided by the Examples and Comparative Examples were fully charged at 4C and discharge at 1C for 10 times, then they were fully charged at 4C, subsequently, the negative electrode plates were disassembled to observe the state of lithium precipitation on the surface of the negative electrode plates. If the area of the lithium precipitation area on the surface of the negative electrode was less than 5%, it was considered slight lithium precipitation. If the area of the lithium precipitation area on the surface of the negative electrode was between 5% and 40%, it was considered moderate lithium precipitation. If the area of the lithium precipitation area on the surface of the negative electrode was greater than 40%, it was considered severe lithium precipitation.
The steps of testing the cycling performance include: at 25° C., the lithium-ion batteries provided by the Examples and Comparative Examples were charged at a rate of 1C and discharged at a rate of 1C, and a full charge and discharge cycle test was conducted until the capacity of the lithium-ion battery decays to 80% of the initial capacity, and the number of cycles was recorded.
From the comparison among Examples 1-24, and Comparative Examples 1-3, it can be seen that when the lithium ion migration kinetic coefficient Fc of the positive electrode coating and the lithium ion migration kinetic coefficient Fa of the negative electrode coating satisfy: 0.25≤Fc/Fa≤5, the lithium-ion battery has good dynamic performance and cycling performance.
Comparing Example 1 with Example 3, it can be seen that when the lithium ion migration kinetic coefficient Fc of the positive electrode coating and the lithium ion migration kinetic coefficient Fa of the negative electrode coating satisfy: 0.25≤F/Fa≤5, controlling the average particle size of the positive electrode active material can further improve the comprehensive performance of the lithium-ion battery.
Comparing Example 4 with Example 5, it can be seen that when the lithium ion migration kinetic coefficient Fc of the positive electrode coating and the lithium ion migration kinetic coefficient Fa of the negative electrode coating satisfy: 0.25≤F/Fa≤5, further modification of the positive electrode active material can further improve the comprehensive performance of the lithium-ion battery.
Comparing Example 21, Example 22, and Example 23, it can be seen that when the lithium ion migration kinetic coefficient Fc of the positive electrode coating and the lithium ion migration kinetic coefficient Fa of the negative electrode coating satisfy: 0.25≤F/Fa≤5, and the compaction density of the positive electrode coating is in a range from 3.0 g/cm3 to 3.8 g/cm3, the comprehensive performance of the lithium-ion battery can be further improved.
The embodiment of the present application also provides an electrical device, including a lithium-ion battery in the aforementioned embodiments.
Obviously, the above embodiments are only provided as examples for the purpose of clarifying, rather than limiting the embodiments. For ordinary technical personnel in this field, different forms of changes or modifications can be made based on the above explanations. There is no need and cannot be an exhaustive list of all implementations here. The obvious changes or variations arising from this are still within the scope of protection of the present invention.
| Number | Date | Country | Kind |
|---|---|---|---|
| 202310093288.0 | Feb 2023 | CN | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/CN2023/115022 | 8/25/2023 | WO |
