Patent Application
20250038193
The present application relates to the field of cathode material and, in particular, to composite cathode material and method for preparing the same, lithium ion battery.
Lithium ion battery is widely used in electric vehicles and consumer electronics products due to the advantages of high energy density, high output power, long cycle life, and little environmental pollution. It has been a research direction for developers to improve the rate performance, thermal stability, and cycling stability of a lithium ion battery. In the nickel-rich cathode material of the prior art, the particles crack after a long cycle such that the internal structure tend to directly exposure, affecting the long cycle stability of the cathode material and the rate performance of the lithium ion battery.
Further, the preparation method of the cathode material of the prior art, for example, may employ a liquid phase mixing for coating material, but the liquid phase method tend to damage the surface structure of the cathode material. There is more cationic disorder of Li/Ni in the material, resulting poor structural stability. And the coating material is easily lost with the solution, thus it is difficult to control the coating amount. A solid phase coating may also be employed, but the cathode material coated by the solid phase has excessive residual lithium, affecting the processing performance of the cathode material, and the coating is non-uniformity.
Based on this, it is desirable to develop a composite cathode material and a method for preparing the same to improve coating uniformity, thereby improving the rate performance and cycling stability of lithium ion battery, reducing production costs.
In view of this, the present application provides a composite cathode material and a method for preparing the same, a lithium ion battery, which may improve the coating uniformity, precisely control the amount of coating, improve the rate performance and cycling stability of the lithium ion battery, and reduce production costs.
In a first aspect, an embodiment of the present application provides a composite cathode material including:
In the above solution, the coating layer is distributed on the surface of the active material, the coating layer containing a phosphate compound, such that the cathode material has a low impedance, a high rate performance, a superior thermal stability, and excellent cycling stability. Moreover, after a modification by coating, the surface defects of the small particles are restored, the cationic disorder of Li/Ni decreases, and the particle hardness increases substantially.
In conjunction with the first aspect, in a possible embodiment, the composite cathode material satisfies at least one of the following conditions a to c:
In conjunction with the first aspect, in a feasible embodiment, the composite cathode material satisfies at least one of the following conditions a to e:
In the present application, the particle size represents the largest linear dimension of the particle, that is, the maximum linear distance between two points on the circumference of the particle.
In the present application, D10 represents the particle size when the cumulative particle size distribution of the particles reaches 10%, meaning that the particles having a particle size less than or equal to D10 account for 10% of the total particles. In the present application, D50 represents the particle size when the cumulative particle size distribution of the particles reaches 50%, meaning that the particles having a particle size less than or equal to D50 account for 50% of the total particles.
In a second aspect, the present application provides a method for preparing the composite cathode material, where the method includes the following:
In the present solution, the use of an atomizing coating process may avoid the filtration loss due to dissolving the coating material in the solution by using a conventional liquid phase coating, the accuracy of the coating amount can be improved. While coating uniformity and reactivity with respect to the solid phase coating are improved. During the atomizing coating process, in one aspect, the phosphate coating solution forms droplets with a micro-nano structure with higher adsorption, which can improve the reactivity of the active material during the mixing process; the coating material is more easily and uniformly embedded in pores of the active material (lithium nickel cobalt aluminum composite oxide or lithium nickel cobalt manganese composite oxide); the surface defects of the active material are restored; a homogeneous coating is formed; and particle hardness is improved. Forming a high lithium ionic conductivity network on the surface of the primary particle of the active material may significantly reduce material impedance, optimize electrochemical performance of the material. On the other aspect, the small particles in the composite cathode material have a larger surface area, and more surface defects are formed during the washing process, thus the particle hardness of the small particles is low compared to the large particles. The hardness of the small particle can be greatly improved by atomizing and coating with phosphate, making Cs10/Cs50≥0.7. Further, during battery electrode preparation, the small particles can have a higher compressive strength, resulting in a higher packing density of the electrodes, thereby increasing the energy density of the battery.
In conjunction with the second aspect, in a feasible embodiment, the method satisfies at least one of the following conditions a to d:
In conjunction with the second aspect, in a feasible embodiment, the method satisfies at least one of the following conditions a to d:
In conjunction with the second aspect, in a feasible embodiment, before the coating a coating solution including phosphate ions and lithium ions with the filter cake of active material in an atomization manner, the method further includes:
In conjunction with the second aspect, in a feasible embodiment, the method satisfies at least one of the following conditions a to e:
In conjunction with the second aspect, in a feasible embodiment, the method satisfies at least one of the following conditions a to b:
In conjunction with the second aspect, in a feasible embodiment, after the coating process, the method further includes:
In a third aspect, the present application provides a lithium ion battery including a positive electrode, a negative electrode, a separator, a non-aqueous electrolyte, and a case, where the positive electrode includes a current collector and a composite cathode material, as described in the first aspect above or a composite cathode material as prepared by the method for preparing the composite cathode material as described in the second aspect above, coated on the current collector.
The technical solutions of the present application have at least the following beneficial effects:
The composite cathode material provided by the present application is distributed with a coating layer on the surface of the active material, where the high degree of crystallization of the active material is advantageous to increase the conductivity of the cathode material. The surface of and the gap between the active materials are filled or coated with the phosphate compound, which may significantly improve the conductivity of the active material. The coated cathode material has a low impedance, a high rate performance, a superior thermal stability, and excellent cycling stability. Moreover, the composite cathode material has been modified by the coated layer, resulting restoring the surface defects of active material, improving particle hardness, and facilitating to improve processing performance of the material.
The method for preparing the composite cathode material provided by the present application employs an atomizing coating process, which can avoid the filtration loss due to dissolving the coating material in the solution by using a conventional liquid phase coating, the accuracy of the coating amount can be improved. While coating uniformity and reactivity with respect to the solid phase coating are improved. During the atomizing coating process, in one aspect, the phosphate coating solution forms droplets with a micro-nano structure with higher adsorption, which can improve the reactivity of the active material during the mixing process; the coating material is more easily and uniformly embedded in pores of the active material (lithium nickel cobalt aluminum composite oxide or lithium nickel cobalt manganese composite oxide); the surface defects of the active material are restored; a homogeneous coating is formed; and particle hardness is improved. Forming a high lithium ionic conductivity network at the surface of the primary particle of the active material may significantly reduce material impedance, optimize electrochemical performance of the material. The preparation process is simple, suitable for mass production, and reduce the cost.
The following are preferred embodiments and examples of the present application. It should be noted that, for those of ordinary skill in the art, many modifications and adaptations may be made without departing from the principles of the embodiments of the present application, which are also considered to fall within the scope of the embodiments of the present application.
A first aspect of the present application provides a composite cathode material including an active material and a coating layer distributed on a surface of the active material; where the active material has a chemical formula of Lia(NixCoyRz)1-bMbO2, where 0.9≤a≤1.10, x+y+z=1, 0.8≤x≤0.99, 0≤y≤0.15, 0≤z≤0.1, 0≤b≤0.1; R includes Al and/or Mn, M includes a metallic element; the coating layer includes a phosphate compound; the composite cathode material has a particle hardness Cs≥50 Mpa and satisfies the following relationship: Cs10/Cs50≥0.7; where Cs10 is the hardness of particles with a particle size D10, and Cs50 is the hardness of particles with a particle size D50.
Optionally, M includes a dopant element, M includes at least one of Mg, Sr, Ca, Ba, Ti, Zr, Mn, Y, Gd, W, Nb, La, and Mo.
As an optional technical solution of the present application, the ratio of X-ray diffraction peak intensity I003 of (003) crystal plane to X-ray diffraction peak intensity I104 of (104) crystal plane of the active material is 1.25 or more; specifically may be 1.25, 1.26, 1.27, 1.28, 1.29, 1.30, 1.32, 1.35, 1.40, etc., which are not limited herein. It is to be appreciated that the greater the ratio of the X-ray diffraction peak intensity of the crystal plane of the active material, the higher the degree of crystallization of the active material, which facilitates increasing the conductivity of the cathode material.
As an optional technical solution of the present application, the Li ion of the active material has an occupation ratio of 98% or more in the Li site (hereinafter, also referred to as “Li site occupation ratio of Li ion”). It is noted that the Li site occupation ratio of Li ion represents the percentage of the Li ions occupying the Li site relative to all Li sites in the Li layer of the active material crystal. It is to be appreciated that the higher the Li site occupation ratio of Li ion, the higher the discharge capacity of the active material. When the Li site occupation ratio of Li ion of the active material is lower, the Li ions in the Li position become less, there are Ni, Co, Al present in the Li position, thus cationic disorder of Li/Ni tend to occur, the crystal structure of the active material becomes defective, and the discharge capacity and cycling characteristics of the active material decrease. Moreover, Li ions leaving the crystal structure may be present in the form of lithium carbonate or the like, causing gas generation, affecting the safety performance of the battery.
In the present embodiment, the surface of the active material coating the phosphate compound, the phosphate compound can increase the ionic conductivity of the active material. It is to be appreciated that the surface of and the gap between the active materials are filled or coated with the phosphate compound, which may significantly increase the ionic conductivity of the active material. The coated cathode material has a low impedance, a high rate performance, a superior thermal stability, and excellent cycling stability.
Optionally, the phosphate compound includes at least one of Li3PO4 and LiXPO4, where X includes at least one of Na, K, Al, Sr, Zr, B, Mg, Ba, Ca, Co, and W, and the X is derived from a metal phosphate compound.
Optionally, the amount of the phosphate compound in the coating layer is from 0.05 wt % to 1.5 wt % of the mass of the active material, specifically may be 0.05 wt %, 0.08 wt %, 0.1 wt %, 0.2 wt %, 0.5 wt %, 0.8 wt %, 1.0 wt %, 1.2 wt %, or 1.5 wt %, etc., or other values within the above ranges, which are not limited herein.
Optionally, the composite cathode material has an average particle size of 3 μm to 20 μm; specifically 3 μm, 4 μm, 5 μm, 6 μm, 7 μm, 8 μm, 10 μm, 12 μm, 15 μm, 18 μm, or 20 μm, etc., or other values within the above ranges, which are not limited herein. Controlling the particle size of the composite cathode material within the ranges described above facilitates increasing structural stability, thermal stability, and long cycle stability of the cathode material.
As an optional technical solution to the present application, the powder conductivity of the composite cathode material at 20 kN/cm2 pressurization is 0.001 S/cm-0.1 S/cm, which ensure the charging and discharging capacity of the composite cathode material.
As an optional technical solution to the present application, the specific surface area of the composite cathode material is 0.2 m2/g to 2.0 m2/g. Specifically may be 0.2 m2/g, 0.5 m2/g, 0.7 m2/g, 0.9 m2/g, 1.1 m2/g, 1.3 m2/g, 1.5 m2/g, 2.0 m2/g, etc. Applicants have discovered, by numerous experimentation, that if the specific surface area of the composite cathode material is controlled to be within the above range, it facilitate to improve cycling performance of the lithium ion battery made of the cathode material.
In a second aspect, the present application further provides a method for preparing the composite cathode material, as shown in
As an optional technical solution of the present application, the primary component includes at least one of NixCoyRzO, NixCoyRz(OH)2, NixCoyRzOOH, where x+y+z=1, 0.8≤x≤0.99, 0≤y≤0.15, 0≤z≤0.1; R includes Al and/or Mn.
The molar content of Ni in NixCoyRzO, NixCoyRz(OH)2, and NixCoyRzOOH is 0.8≤x≤0.99, where the value range of x may specifically be 0.8, 0.82, 0.84, 0.86, 0.88, 0.9, 0.92, 0.94, 0.96, 0.98, or 0.99, etc.
The molar content of Co in NixCoyRzO, NixCoyRz(OH)2, and NixCoyRzOOH is 0≤y≤0.15, where the value range of y may specifically be 0, 0.01, 0.02, 0.05, 0.06, 0.08, 0.1, 0.11, 0.12, 0.14, or 0.15, etc.
The molar content of R in NixCoyRzO, NixCoyRz(OH)2, and NixCoyRzOOH is 0≤z≤0.1, where the value range of z may specifically be 0, 0.01, 0.02, 0.03, 0.04, 0.05, 0.06, 0.07, 0.08, 0.09, or 0.1, etc.
Specifically, the primary component has an average particle size of 3 μm to μm, specifically 3 μm, 5 μm, 7 μm, 9 μm, 10 μm, 12 μm, 14 μm, 15 μm or 20 μm, etc., or other values within the above ranges, which are not limited herein.
Applicants have discovered, by numerous experimentation, that if the average particle size of the primary component is controlled to be within the range of 3 μm to 20 μm, it is able to effectively control the particle size of the active material, avoiding the cracking of the active material during cycling, facilitating to improve structural stability, thermal stability, and long cycle stability of the active material.
As an optional technical solution of the present application, the secondary component includes at least one of M oxides, M hydroxides, or M phosphates, where M is a metallic element.
As an optional technical solution of the present application, the lithium compound is selected from at least one of lithium hydroxide, lithium carbonate, lithium acetate, lithium nitrate, and lithium oxalate.
As an optional technical solution of the present application, the ratio of the sum of the molar content of Ni, Co, and R to the molar content of Li is 1:(0.9-1.10) in the primary component; specifically may be 1:0.9, 1:0.95, 1:0.96, 1:0.97, 1:0.98, 1:0.99, 1:1.00, 1:1.01, 1:1.02, 1:1.05, 1:1.06, 1:1.07, 1:1.08, 1:1.09, or 1:1.10, etc., or other values within the above ranges, which are not limited herein. When the ratio is too small, it indicates that there is an excess of Li, which leads to the formation of Li2MO3 phase on the surface of the material, decreasing the active Li+ content, resulting in a reduction in capacity, and gas generation during the cycling. When the ratio is too large, there are many Li vacancies. Ni2+ enters the Li layer to form a cationic disorder layer, reducing material structural stability, which leads to material degradation, and decreasing cycling performance.
As an optional technical solution of the present application, the sintered product is an active material, the conditions for obtaining the sintered product are: heating up to 650° C. to 850° C. for sintering for 5 h to 20 h in a flowing oxygen atmosphere. Lithium nickel cobalt aluminum composite oxide or lithium nickel cobalt manganese complex oxide is obtained by sufficiently sintering.
Specifically, the lithium content in the lithium compound on the surface of the lithium nickel cobalt aluminum composite oxide or the lithium nickel cobalt manganese composite oxide is 0.6 wt % or less of the total composite oxide, i.e., the lithium in the lithium compound on the surface of the lithium nickel cobalt aluminum composite oxide or the lithium nickel cobalt manganese composite oxide has migrated inside the composite oxide. Less lithium content on the surface may inhibit gas generation phenomenon during cycling of the cathode material.
Optionally, the oxygen content in the oxygen-containing atmosphere is 99% or more, so that each of metal elements are fully oxidized.
Optionally, the temperature of the sintering may be 650° C., 680° C., 700° C., 720° C., 750° C., 780° C., 800° C., 820° C., or 850° C., etc., or other values within the above range. Preferably, the temperature of the sintering is 700° C. to 800° C.
Optionally, the time of the sintering may specifically be 5 h, 7 h, 9 h, 11 h, 13 h, 15 h, 17 h, 19 h, 20 h, etc., or other values within the above range. Preferably, the time of the sintering is 8 h to 15 h.
As an optional technical solution of the present application, the ratio of X-ray diffraction peak intensity I003 of (003) crystal plane to X-ray diffraction peak intensity I104 of (104) crystal plane of the active material is 1.25 or more; specifically may be 1.25, 1.26, 1.27, 1.28, 1.29, 1.30, 1.32, 1.35, 1.40, etc., which are not limited herein. It is to be appreciated that the greater the ratio of X-ray diffraction peak intensity of the crystal plane of the active material, the higher the degree of crystallization of the active material, which facilitates increasing the conductivity of the cathode material.
As an optional technical solution of the present application, the Li ion of the active material has an occupation ratio of 98% or more in the Li site (Li site occupation ratio of Li ion). It is noted that the Li site occupation ratio of Li ion represents the percentage of the Li ions occupying the Li site relative to all Li sites in the Li layer of the active material crystal lattice. It is to be appreciated that the higher the Li site occupation ratio of Li ion, the higher the discharge capacity of the active material. When the Li site occupation ratio of Li ion of the active material is lower, the Li ions in the Li position become less, there are Ni, Co, Al present in the Li position, thus cationic disorder of Li/Ni tend to occur. While Li ions leaving the crystal structure may be present in the form of lithium carbonate or the like. By increasing the Li position occupancy rate of Li ions, the cationic disorder of Li/Ni of the material is effectively inhibited, which can significantly increase the structural stability of the active material, improving safety performance.
In step S20, grinding the sintered product, and washing and filtering, resulting a filter cake of active material.
In a specific embodiment, the wash solvent is water, a temperature of washing is 10° C. to 40° C., and a time of the washing is 10 min to 60 min. Specifically, the time of the washing may be 10 min, 20 min, 30 min, 40 min, 50 min, or 60 min, etc., and the temperature of washing may be 10° C., 20° C., 25° C., 30° C., 35° C., or 40° C., etc.
Optionally, the wash solvent is used in an amount of 500 g/L to 2000 g/L. It is noted that the amount of the wash solvent refers to the mass of the sintered product contained in the solvent per liter. Specifically, the amount of the wash solvent may be 500 g/L, 600 g/L, 700 g/L, 800 g/L, 900 g/L, 1000 g/L, 1200 g/L, 1400 g/L, 1500 g/L, 1800 g/L, or 2000 g/L, etc., which are not limited herein. The time of the filtering is 30 min to 150 min, which may be 30 min, 50 min, 60 min, 80 min, 100 min, 120 min, or 150 min, etc.
Preferably, the temperature of the washing is 20° C. to 30° C., the wash solvent is used in an amount of 800 g/L to 1500 g/L, the time of for washing is 20 min to 40 min, and the time of the filtering is 60 min to 120 min. It is to be appreciated that impurities such as lithium carbonate, lithium hydroxide, and the like attached to the surface of the sintered product may be removed as long as the sintered product is sufficiently washed. If the washing is insufficient, resulting in a high surface lithium content of the composite cathode material. During cycling of the battery, the surface residual lithium reacts with the electrolyte to produce a gas, affecting the safety of the battery.
Optionally, the water content of the filter cake of active material resulting from filtration is 5 wt % or less. Preferably, the water content of the filter cake of active material filter cake is 1 wt % or less for reducing the impact of moisture on the properties of the active material.
Optionally, prior to step S20, the method further includes:
Optionally, the phosphorous source includes at least one of HPO3, H3PO2, H3PO4, Li3PO4, and a metal phosphate compound.
Optionally, the metal phosphate compound includes at least one of K3PO4, BPO4, NH4H2PO4, (NH4)2HPO4, Zr(HPO4)2, Na2HPO4, SrHPO4, BaHPO4, Ba3(PO4)2, MgHPO4, Ca(H2PO2)2, Al(H2PO4)3, CoHPO4, or H3P(W3O10)4·nH2O, where n≥1.
Optionally, the soluble lithium compound includes at least one of lithium hydroxide, lithium carbonate, lithium nitrate, lithium chlorate and lithium acetate. Preferably, the soluble lithium compound is lithium hydroxide.
Optionally, in the coating solution, the molar ratio of the lithium ions to the phosphate ions is (0-10):1; specifically may be 0:1, 1:1, 2:1, 3:1, 4:1, 5:1, 6:1, 7:1, 8:1, 9:1, or 10:1, etc., or other values within the above ranges, which are not limited herein. The excess of lithium ion content leads to the excess of the residual lithium content on the material surface; the excess of phosphate content leads to too thick of the coating layer, which affect the capacity and rate capability of the material. Preferably, the molar ratio of lithium ions to phosphate ions is (0-5):1.
As an optional technical solution of the present application, the mass of phosphate in the phosphorous source accounts 0.05 wt % to 1.5 wt % of the filter cake of active material; specifically may be 0.05 wt %, 0.08 wt %, 0.10 wt %, 0.2 wt %, 0.3 wt %, 0.5 wt %, 0.8 wt %, 1.0 wt %, 1.2 wt %, 1.3 wt % or 1.5 wt %, etc., or other values within the above range. If the phosphate mass in the phosphorous source is excessive, the phosphate coating on the active material surface will be excessive, reducing material capacity. Preferably, the mass of phosphate in the phosphorous source accounts 0.1 wt % to 1 wt % of the filter cake of active material.
As an optional technical solution of the present application, the total mass of the phosphorous source and the soluble lithium compound accounts 1.5 wt % to 45 wt % of the coating solution, specifically may be 1.5 wt %, 5 wt %, 8 wt %, 10 wt %, 15 wt %, 20 wt %, 25 wt %, 30 wt %, 35 wt %, 40 wt % or 45 wt %, etc., or other values within the above range.
Further, the mass of the phosphorous source accounts 1.5 wt % to 30 wt % in the coating solution, specifically may be 1.5 wt %, 5 wt %, 8 wt %, 10 wt %, 15 wt %, 20 wt %, 25 wt % or 30 wt %, etc., or other values within the above range. The mass of the soluble lithium compound accounts 0 wt % to 15 wt % in the coating solution, specifically may be 0 wt %, 1 wt %, 2 wt %, 3 wt %, 4 wt %, 5 wt %, 6 wt %, 7 wt %, 8 wt %, 9 wt %, 10 wt %, 12 wt % or 15 wt %, etc., or other values within the above range.
In step S30, coating the coating solution including phosphate ions and lithium ions with the filter cake of active material in an atomization manner to yield a composite cathode material.
As an optional technical solution of the present application, the atomization manner includes at least one of ultrasonic atomization and high pressure atomization. It is to be understood that coating active material by atomization, as compared to conventional liquid phase coating, may reduce loss of phosphorous source and/or soluble lithium compound in the coating solution, and may improve the accuracy of coating amount of the coating material; and as compared to conventional solid phase coating, may improve coating uniformity and reactivity.
In the coating process, the coating solution forms droplets with a micro-nano structure by atomization, having higher adsorption, which has higher reactivity with the active material when mixed with them. The coating solution droplets are uniformly embedded or impregnated into the pores of the active material, restoring surface defects of the active material, and forming homogeneous coating. Forming a high lithium ionic conductivity network on the surface of the primary particle of the active material may significantly reduce the active material impedance, optimize electrochemical performance of the active material.
During the coating process, the temperature is controlled to be 50° C. to 100° C., specifically may be 50° C., 55° C., 60° C., 65° C., 70° C., 75° C., 80° C., 85° C., 90° C., 95° C., or 100° C., etc., which are not limited herein. During the gradient heating process, the coating solution is mixed with the filter cake of the active material and dried, the coating material sufficiently reacts with the active material, thus the reactivity of the coating and the active material is improved, and the coating effect is improved.
During the coating process, the heat preservation is controlled to be 5 min to 60 min; specifically may be 5 min, 10 min, 15 min, 20 min, 25 min, 30 min, 35 min, 40 min, 45 min, 50 min, or 60 min, etc., which are not limited herein.
Optionally, after step S30, the method further includes:
Drying the composite cathode material, where a temperature of the drying is controlled to be 150° C. to 210° C. and a heat preservation is controlled to be 10 h to 24 h.
As an optional technical solution of the present application, the temperature of the drying may be 150° C., 155° C., 160° C., 165° C., 170° C., 175° C., 180° C., 185° C., 190° C., 195° C., 200° C., or 210° C., etc., which are not limited herein. The heat preservation specifically may be 10 h, 12 h, 14 h, 15 h, 17 h, 18 h, 19 h, 20 h, 22 h, or 24 h, etc., which are not limited herein.
As an optional technical solution of the present application, the moisture content of the dried composite cathode material is less than or equal to 0.04 wt %. As a result, the moisture of the composite cathode material is reduced, improving the processing performance of the composite cathode material.
It is to be noted that, in the present embodiment, during the coating and then drying processes, the coating material is sufficiently mixed with the active material and dried, improving the reactivity and coating uniformity, by controlling process parameters such as atomizing liquid jet velocity, mixing device speed, temperature, and the like, in a gradient heating manner.
In the present solution, the use of an atomizing coating process may avoid the filtration loss due to dissolving the coating material in the solution by using a conventional liquid phase coating, the accuracy of the coating amount can be improved. While coating uniformity and reactivity with respect to the solid phase coating are improved. During the atomizing coating process, in one aspect, the phosphate coating solution forms droplets with a micro-nano structure with higher adsorption, which can improve the reactivity of the active material during the mixing process; the coating material is more easily and uniformly embedded in pores of the active material (lithium nickel cobalt aluminum composite oxide or lithium nickel cobalt manganese composite oxide); the surface defects of the active material are restored; a homogeneous coating is formed. Forming a high lithium ionic conductivity network at the surface of the primary particle of the active material may significantly reduce material impedance, optimize electrochemical performance of the material.
In a third aspect, an embodiment of the present application further provides a lithium ion battery including a positive electrode, a negative electrode, a separator, a non-aqueous electrolyte, and a case, where the positive electrode includes a current collector and the composite cathode material, as described above or the cathode material as prepared by the method for preparing the composite cathode material as described above, coated on the current collector.
The following several examples further illustrate the embodiments of the present application. The embodiments herein are not limited to the specific examples described below. Variations may be made as appropriate within the scope of the independent claims.
Ni0.88Co0.09Al0.03(OH)2 and LiOH·H2O were mixed by a high speed mixer in a molar ratio of Li/NiCoAl of 1.04:1, resulting in a mixture with an average particle size of 11.0 μm;
The composite cathode material prepared by this example includes an active material and a lithium phosphate coating layer on the surface of the active material; where the composite cathode material has an average particle size of 11.3 μm, a specific surface area of 0.75 m2/g, and a powder conductivity of 0.056 S/cm2.
Ni0.88Co0.09Al0.03(OH)2, LiOH·H2O, and Zr(OH)4 were mixed by a high speed mixer in a molar ratio of Li/NiCoAl of 1.04:1, resulting in a mixture with an average particle size of 11.0 μm, where the molar ratio of Zr to the total amount of Ni, Co, and Al is 0.005:1;
The composite cathode material prepared by this example includes an active material and a lithium phosphate coating layer on the surface of the active material; where the composite cathode material has an average particle size of 11.6 μm, a specific surface area of 0.64 m2/g, and a powder conductivity of 0.068 S/cm2.
Ni0.99Co0.01(OH)2, LiOH·H2O, and Zr(OH)4, Ti(OH)4, were mixed by a high speed mixer in a molar ratio of Li/NiCo of 1:1, resulting in a mixture with an average particle size of 5.0 μm, where the molar ratio of Zr and Ti to Ni and Co is 0.005:1, and the molar ratio of Zr and Ti is 3:2;
The composite cathode material prepared by this example includes an active material and a strontium lithium phosphate coating layer on the surface of the active material; where the composite cathode material has an average particle size of 5.2 μm, a specific surface area of 0.83 m2/g, and a powder conductivity of 0.045 S/cm2.
Ni0.80Co015Al0.05(OH)2 and LiOH·H2O were mixed by a high speed mixer in a molar ratio of Li/NiCoAl of 1.04:1, resulting in a mixture with an average particle size of 15.0 μm;
The composite cathode material made prepared by this example includes an active material and a zirconium lithium phosphate coating layer on the surface of the active material; where the composite cathode material has an average particle size of 15.3 μm, a specific surface area of 0.92 m2/g, and a powder conductivity of 0.057 S/cm2.
Ni0.88Co0.06M0.03Al0.03(OH)2, LiOH·H2O, and lithium acetate were mixed by a high speed mixer in a molar ratio of Li/NiCoMnAl of 1.04:1, resulting in a mixture with an average particle size of 11.0 μm;
The composite cathode material prepared by this example includes an active material and a lithium phosphate coating layer on the surface of the active material; where the composite cathode material has an average particle size of 11.9 μm, a specific surface area of 1.01 m2/g, and a powder conductivity of 0.082 S/cm2.
Ni0.91Co0.04Al0.05(OH)2 and LiOH·H2O were mixed by a high speed mixer in a molar ratio of Li/NiCoAl of 1.04:1, resulting in a mixture with a particle average particle size of 11.0 μm;
The composite cathode material prepared by this example includes an active material and a lithium phosphate coating layer on the surface of the active material; where the composite cathode material has an average particle size of 11.6 μm, a specific surface area of 1.13 m2/g, and a powder conductivity of 0.039 S/cm2.
Ni0.83Co0.11Mn0.06(OH)2 and LiOH·H2O were mixed by a high speed mixer in a molar ratio of Li/NiCoMn of 1.04:1, resulting in a mixture with an average particle size of 11.0 μm;
The composite cathode material prepared by this example includes an active material and a lithium phosphate coating layer on the surface of the active material; where the composite cathode material has an average particle size of 11.5 μm, a specific surface area of 0.65 m2/g, and a powder conductivity of 0.060 S/cm2.
Ni0.88Co0.09Al0.03(OH)2 and LiOH·H2O were mixed by a high speed mixer in a molar ratio of Li/NiCoAl of 1.04:1, resulting in a mixture with an average particle size of 11.0 μm;
Ni0.88Co0.09Al0.03(OH)2 and LiOH·H2O were mixed by a high speed mixer in a molar ratio of Li/NiCoAl of 1.04:1, resulting in a mixture with an average particle size of 11.0 μm;
Ni0.88Co0.09Al0.03(OH)2 and LiOH·H2O were mixed by a high speed mixer in a molar ratio of Li/NiCoAl of 1.04:1, resulting in a mixture with an average particle size of 11.0 μm;
The cathode material was subjected to particle size testing using a Malvern Mastersizer 2000 laser particle sizer to obtain the particle size distribution and average particle size.
The particle hardness of the composite cathode material was tested using an Shimadzu Dynamic Ultra Microscopy Hardness Tester.
The surface area testing was performed on the cathode material using the Micromeritics Tristar 3020 type specific surface area and the pore size analyzer. A mass of powder is weighed, fully degassed under vacuum heating conditions. After surface adsorption being removed, the specific surface area of the particles is calculated by adsorption of the amount of nitrogen using a nitrogen adsorption process.
The cathode material was subjected to a powder conductivity test using a FT-8100 series of four probe method. A mass of powder is weighed, which is compacted at a pressure of 20 kN/cm2, and the material powder conductivity is tested using a four-probe powder resistance tester.
Preparation of a 2032 coin cell: the cathode prepared by each of the examples, conductive carbon, and polyvinylidene fluoride were added to N-methylpyrrolidone in a ratio of 96:2:2, stirred to obtain slurry. The slurry was coated on aluminum foil and dried to be as a cathode. A lithium sheet was used as the negative electrode to prepare a 2032 type coin cell.
Discharge capacity, cycle performance, and rate performance test: electrical performance testing was performed at 25° C., 2.5 V to 4.3 V using an LAND battery test system. The initial charging was conducted to 4.3 V by a current of 0.1 C rate, and the initial discharging was conducted to 2.5 V by a current of 0.1 C rate. Then the cycle of charging and discharging was repeated, and the capacity retention of 50 cycles was recorded, where the charging was conducted to 4.3 V by a current of 0.5 C rate and the discharging was conducted to 2.5 V by a current of 1 C rate during the cycle.
DCR test: electrical performance testing was conducted at 25° C., 2.5 V to 4.3 V using an Arbin cell test system. In the initial cycle, the charging was conducted to 4.3 V by a current of 0.5 C rate, and the discharging was conducted to 2.5 V by a current of 1 C rate. The value of the DCR was calculated by dividing the voltage drop value 10 seconds after start of the self-discharging by the current value.
EIS test: Electrochemical impedance test was performed on a 2032 type coin cell at 100% SOC at 25° C. using a multichannel potentiostat (Bio-Logic, VMP3) at a frequency of 1 MHz to 1 mHz.
SEM test: The surface topography of the material was scanned by Hitachi S4800 scanning electron microscope.
EDS test: The electron microscopy was performed on the surface of the material by Hitachi S4800 scanning electron microscope.
Test of the Li position occupancy rate of Li ions: the prepared cathode material was determined by the powder X-ray diffraction using CuKα radiation, resulting in an X-ray diffraction pattern of the cathode material, then the Li position occupancy rate of Li ion was calculated by Rietveld analysis. The Rietveld analysis employed the method of: a crystal structure model was assumed for fitting the X-ray diffraction pattern obtained by the crystal structure model with the actual measured X-ray diffraction pattern. The lattice constant parameters of the crystal structure model was adjusted for conforming the two X-ray diffraction patterns, and calculating the Li position occupancy of the Li ions by the resulting lattice constant data.
The peak intensity ratio of the X-ray diffraction peak of (003) crystal plane/the X-ray diffraction peak of (104) crystal plane: the prepared cathode material was determined by the powder X-ray diffraction using CuKα radiation, resulting in an X-ray diffraction pattern of the cathode material, then the Li position occupancy rate of Li ion was calculated by the Rietveld analysis. The Rietveld analysis employed the method of: a crystal structure model was assumed for fitting the X-ray diffraction pattern obtained by the crystal structure model with the actual measured X-ray diffraction pattern. The lattice constant parameters of the crystal structure model was adjusted for conforming the two X-ray diffraction patterns, and calculating the ratio by the resulting X-ray diffraction peak intensity of (003) and (104) crystal planes.
It can be seen from
It can be seen from
As shown in
It can be seen from the comparison of the experimental results shown in Table 1, the samples in which the filter cake is coated by phosphate have superior particle hardness, discharge capacity, cycling performance, and rate performance.
From the Li position occupancy rate of Li ions and the peak intensity ratio of the X-ray diffraction peak of (003) crystal plane/the X-ray diffraction peak of (104) crystal plane of Example 1 and Comparative Example 1, it can be seen that the sample in which filter cake is coated by phosphate has a higher Li position occupancy rate of Li ion concentration and higher peak intensity ratio of the X-ray diffraction peak of (003) crystal plane/the X-ray diffraction peak of (104) crystal plane, showing that the sample in which the filter cake is coated by phosphate has a lower cationic disorder of Li/Ni, and better structural stability and particle hardness.
Comparative Example 2 employs a liquid phase coating, partial phosphorous source and soluble lithium compound are lost with the solution. Thus the coating amount on the surface of the material is not easily controllable, resulting in a great difference in the specific surface area between of the material before and after coating, affecting the stability of the material structure.
Comparative Example 3 does not wash the sintered product during the preparation process, resulting in higher residual lithium on the surface of the cathode material, and resulting in increased directive current resistance, impacting capacity and rate performance of the material.
While the present application has been disclosed by preferred embodiments, it is not to limit the claims. Those skilled in the art can make various changes and modifications without departing from the concepts of the present application.
Therefore, the scope of the present application shall be accorded the scope as defined by the following claims.
| Number | Date | Country | Kind |
|---|---|---|---|
| 202210142540.8 | Feb 2022 | CN | national |
The present application is a National Stage of International Application No. PCT/CN2022/076861, filed Feb. 18, 2022, which claims the benefit of Chinese Patent Application No. 202210142540.8 filed with the China Patent Office on Feb. 16, 2022 with the title of “Composite Cathode Material and Method for Preparing the Same, Lithium Ion Battery,” both of which are incorporated herein by reference in their entireties.
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/CN2022/076861 | 2/18/2022 | WO |
