WO2016180288A1 - 制备具有铝元素梯度分布的镍钴铝前驱材料和正极材料的方法 - Google Patents

制备具有铝元素梯度分布的镍钴铝前驱材料和正极材料的方法 Download PDF

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WO2016180288A1
WO2016180288A1 PCT/CN2016/081350 CN2016081350W WO2016180288A1 WO 2016180288 A1 WO2016180288 A1 WO 2016180288A1 CN 2016081350 W CN2016081350 W CN 2016081350W WO 2016180288 A1 WO2016180288 A1 WO 2016180288A1
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aluminum
solution
nickel
cobalt
complexing agent
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French (fr)
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吴层
谭潮溥
严亮
黄殿华
陈瑞祥
张郑
袁昌杰
骆宏钧
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广州锂宝新材料有限公司
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Priority to KR1020177019081A priority Critical patent/KR101952210B1/ko
Priority to PL16792138T priority patent/PL3297072T3/pl
Priority to EP16792138.6A priority patent/EP3297072B1/en
Priority to JP2017548519A priority patent/JP6395951B2/ja
Priority to US15/538,131 priority patent/US10329162B2/en
Publication of WO2016180288A1 publication Critical patent/WO2016180288A1/zh

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    • C01—INORGANIC CHEMISTRY
    • C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
    • C01G53/00—Compounds of nickel
    • C01G53/006—Compounds containing, besides nickel, two or more other elements, with the exception of oxygen or hydrogen
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
    • C01G53/00—Compounds of nickel
    • C01G53/40—Nickelates
    • C01G53/42—Nickelates containing alkali metals, e.g. LiNiO2
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/13—Electrodes for accumulators with non-aqueous electrolyte, e.g. for lithium-accumulators; Processes of manufacture thereof
    • H01M4/139—Processes of manufacture
    • H01M4/1391—Processes of manufacture of electrodes based on mixed oxides or hydroxides, or on mixtures of oxides or hydroxides, e.g. LiCoOx
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/13—Electrodes for accumulators with non-aqueous electrolyte, e.g. for lithium-accumulators; Processes of manufacture thereof
    • H01M4/139—Processes of manufacture
    • H01M4/1393—Processes of manufacture of electrodes based on carbonaceous material, e.g. graphite-intercalation compounds or CFx
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/36—Selection of substances as active materials, active masses, active liquids
    • H01M4/48—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides
    • H01M4/485—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides of mixed oxides or hydroxides for inserting or intercalating light metals, e.g. LiTi2O4 or LiTi2OxFy
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/36—Selection of substances as active materials, active masses, active liquids
    • H01M4/48—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides
    • H01M4/52—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides of nickel, cobalt or iron
    • H01M4/525—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides of nickel, cobalt or iron of mixed oxides or hydroxides containing iron, cobalt or nickel for inserting or intercalating light metals, e.g. LiNiO2, LiCoO2 or LiCoOxFy
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
    • C01P2002/00—Crystal-structural characteristics
    • C01P2002/70—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data
    • C01P2002/72—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data by d-values or two theta-values, e.g. as X-ray diagram
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
    • C01P2004/00—Particle morphology
    • C01P2004/01—Particle morphology depicted by an image
    • C01P2004/03—Particle morphology depicted by an image obtained by SEM
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
    • C01P2004/00—Particle morphology
    • C01P2004/30—Particle morphology extending in three dimensions
    • C01P2004/32—Spheres
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
    • C01P2006/00—Physical properties of inorganic compounds
    • C01P2006/40—Electric properties
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M2004/026—Electrodes composed of, or comprising, active material characterised by the polarity
    • H01M2004/028—Positive electrodes
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
    • Y02E60/10—Energy storage using batteries

Definitions

  • the present invention relates to the field of lithium ion battery manufacturing, and in particular to a method of preparing a nickel cobalt aluminum precursor material and a positive electrode material having a gradient distribution of aluminum elements.
  • lithium ion batteries have been widely used in various mobile electronic products and power tools, and positive electrode materials are the key to improving energy density, safety, and cost reduction in lithium ion batteries. Further improving the power density, energy density and improving safety performance of materials is the development direction of cathode materials for lithium ion batteries.
  • LiNiO 2 has attracted attention due to its high capacity, low cost and less pollution.
  • LiNi 1-x Co x O 2 has the advantages of high specific capacity and low cost of LiNiO 2 .
  • it also has good cycle performance, LiNi 1-x Co x O 2 can play a specific capacity of 190mAh / g, but the stability of nickel-cobalt binary material still can not reach the current 3C (home appliances, computers, communications ) Requirements for materials for electronic products and power batteries.
  • Al-doped material represented by nickel-cobalt-aluminum material, LiNi 1-xy Co x Al y O 2 is used as a homogeneous solid solution of LiNiO 2 , LiCoO 2 and LiAlO 2 , and has high energy density and thermal stability. Good, cheap and environmentally friendly, it has become a high-end energy storage material in the 3C field and power battery field.
  • NCA lithium nickel cobalt aluminate material
  • the divalent nickel ions are difficult to oxidize to trivalent, and it is necessary to completely oxidize under a pure oxygen atmosphere.
  • NCA has high water absorption, there is a reaction in the following formula, and battery production needs to be normal production under conditions of 10% humidity or less. Since NCA is easy to release O 2 , CO 2 , etc., the battery is easily inflated, and it is best to use a 18650-type cylindrical battery.
  • the conditions for preparing a structurally stable NCA material and a nickel-cobalt aluminum lithium battery are very demanding.
  • the domestically produced nickel-cobalt-aluminum-lithium cathode material still has defects such as rapid capacity decay, poor rate performance and poor storage performance during charging and discharging. For this reason, in order to meet the mild production process and to prepare nickel-cobalt-aluminum materials with superior performance, it is necessary to develop a novel nickel-cobalt-aluminum precursor.
  • Ni 1-xy Co x Al y (OH) 2 is currently considered to be the best precursor for the preparation of high performance nickel cobalt aluminum.
  • the coprecipitation method is a simple and practical method for preparing LiNiCoAlO 2 and its surface modification.
  • the prepared nickel-cobalt-aluminum precursor often leaves a large amount of sulfate ions difficult to be washed and removed; 2.
  • the aging of 5% wt to 15% wt sodium hydroxide solution of CN 103553152A is favorable.
  • the removal of sulfur, but in the washing process, often leads to the loss of aluminum on the surface, resulting in the lack of aluminum on the surface of the prepared material, which is detrimental to the storage properties, processing properties and electrochemical cycle stability of the positive electrode material.
  • Increasing the doping amount of aluminum can improve the cycle stability, safety performance, processing property and storage performance of the material.
  • Yang-Kook Sun of Hanyang University in Korea developed a new type of gradient lithium-ion battery material in 2008.
  • the core of the material is a nickel-cobalt-manganese ternary material with a high nickel content, and the outer coating layer has a gradually reduced nickel content.
  • This special cathode material exhibits high energy density, long life and good safety.
  • a hydroxide precursor prepared by a coprecipitation method for preparing an Al element gradient distribution is included.
  • the method comprises the steps of: gradually adding an aluminum salt solution to the mixed nickel-cobalt mixed salt solution to control the gradual change of the aluminum concentration in the nickel-cobalt-aluminum mixed salt solution to prepare a hydroxide precursor having a gradient of aluminum element.
  • Al 3+ hardly complexes with ammonia, and Al 3+ is easily hydrolyzed to form a colloid alone without reaching the gradient doping of Al 3+ element in nickel-cobalt-manganese hydroxide. It is advantageous to prepare a high density spherical gradient aluminum doped precursor.
  • the invention provides a method for preparing a spherical nickel hydroxide cobalt aluminum precursor material by a coprecipitation method, and a preparation method of a lithium aluminum cobalt aluminum oxide cathode material for a ladder aluminum type lithium ion battery based on the method, so as to overcome and avoid the prior art.
  • the shortcomings and shortcomings provide a simple and easy to control condition, which can synthesize a lithium aluminum cobalt aluminum oxide cathode material for ladder aluminum type lithium ion battery with excellent electrochemical performance, superior processing performance and storage performance.
  • a method of preparing a spherical nickel hydroxide cobalt aluminum precursor material by a coprecipitation method comprising the steps of:
  • the precursor material is obtained by a precipitation reaction in a reaction vessel, wherein the aqueous nickel cobalt salt solution, the solution containing the complexing agent II, and the sodium hydroxide solution are each fed to the reaction vessel at a constant flow rate.
  • the aluminum-containing complex solution and the solution containing the complexing agent I are added in such a manner that the aluminum-containing complex solution is fed at a constant flow rate to a fixed volume of the solution containing the complexing agent I and Mixing the solution containing the complexing agent I while adding a mixed solution of the aluminum-containing complex solution and the solution containing the complexing agent I to the reaction vessel at a constant flow rate, thereby The aluminum concentration in the mixed solution is gradually increased.
  • the nickel salt in the method is one or more of nickel sulfate, nickel chloride, nickel acetate, and nickel nitrate.
  • the cobalt salt in the method is one or more of cobalt sulfate, cobalt chloride, cobalt acetate and cobalt nitrate.
  • the complexing agent I in the method is one or more of triethanolamine, ammonium fluoride, citric acid, oxalic acid, sodium ethylenediaminetetraacetate and sodium hydroxide.
  • the complexing agent II in the method is one or more of ammonia water, triethanolamine, ammonium fluoride, citric acid, oxalic acid, sodium edetate.
  • the aluminum salt in the method is one or more of aluminum nitrate, aluminum sulfate or aluminum acetate.
  • the molar ratio of the nickel salt to the cobalt salt in the aqueous solution of the nickel-cobalt salt is 1-19.
  • the molar ratio of the nickel salt to the cobalt salt in the aqueous solution of the nickel-cobalt salt may be 1, 2, 3, 4, 5, 6, 7, 8, 9, 10, 11, 12, 13, 14, 15, 16, 17, 18 or 19.
  • the total concentration of the nickel salt and the cobalt salt in the aqueous nickel-cobalt salt solution is 0.2 to 2.5 mol/L, for example, the total of the nickel salt and the cobalt salt in the aqueous solution of the nickel-cobalt salt.
  • the concentration may be 0.2 mol/L, 0.4 mol/L, 0.6 mol/L, 0.8 mol/L, 1.0 mol/L, 1.2 mol/L, 1.4 mol/L, 1.6 mol/L, 1.8 mol/L, 2.0 mol. /L, 2.2 mol/L or 2.5 mol/L.
  • the concentration of the sodium hydroxide solution in the method is 2 to 10 mol/L, for example, the concentration of the sodium hydroxide solution may be 2 mol/L, 3 mol/L, 4 mol/L, 5 mol/L, 6 mol/L, 7 mol/L, 8 mol/L, 9 mol/L or 10 mol/L.
  • the molar ratio of the aluminum element to the complexing agent I in the aluminum-containing complex solution is 1:0.01 to 20.0, for example, the aluminum element in the aluminum-containing complex solution.
  • the molar ratio to the complexing agent I may be 1:0.01, 1:0.05, 1:0.1, 1:0.2, 1:0.3, 1:0.3, 1:0.4, 1:0.5, 1:0.6, 1: 0.7, 1:0.8, 1:0.9, 1:1.0, 1:1.5, 1:2.0, 1:2.5, 1:3.0, 1:3.5, 1:4.0, 1:4.5, 1:5.0, 1:5.5, 1:6.0, 1:6.5, 1:7.0, 1:7.5, 1:8.0, 1:8.5, 1:9.0, 1:10.0, 1:11.0, 1:12.0, 1:13.0, 1:14.0, 1: 15.0, 1:16.0, 1:17.0, 1:18.0, 1:19.0 or 20.0.
  • the concentration of the complexing agent II in the bottom liquid in the method is 0.3 to 2 mol/L, for example, the concentration of the complexing agent II in the bottom liquid may be 0.3 mol/L, 0.4. Mol/L, 0.5 mol/L, 0.6 mol/L, 0.7 mol/L, 0.8 mol/L, 0.9 mol/L, 1.0 mol/L, 1.1 mol/L, 1.2 mol/L, 1.3 mol/L, 1.4 Mol/L, 1.5 mol/L, 1.6 mol/L, 1.7 mol/L, 1.8 mol/L, 1.9 mol/L or 2.0 mol/L.
  • the pH of the bottom liquid in the method is 10-12, for example, the pH of the bottom liquid may be 10, 10.2, 10.4, 10.6, 10.8, 11, 11.2, 11.4, 11.6, 11.8 or 12.
  • a flow rate ratio of the aqueous nickel cobalt salt solution, the solution containing the complexing agent II, the sodium hydroxide solution, and the mixed solution to the reaction vessel is added It is 1: (0.05 to 50): (0.1 to 10): (0.01 to 100).
  • the flow rate of the aluminum-containing complex solution added to the fixed volume of the solution containing the complexing agent I in the method is from 0.1 mL/min to 2000 mL/min.
  • the stirring speed in the reaction vessel in the method is 50 to 1000 rpm.
  • the reaction temperature in the step c) in the method is 20 to 80 °C.
  • the reaction time in the step c) in the method is from 5 to 100 hours.
  • a method for preparing a lithium aluminum cobalt aluminum oxide cathode material for a ladder aluminum type lithium ion battery comprising:
  • the precursor material is uniformly mixed with lithium hydroxide, and then calcined in an oxygen atmosphere furnace, and cooled to room temperature to obtain the ladder aluminum-type lithium ion battery composite cathode material.
  • the step 2) in the method comprises: stirring the precursor material with a sodium chloride solution at a concentration of 20 to 80 ° C and a concentration of 3 to 30 wt% for 10 to 60 minutes; b) adopting The precipitate is washed several times with deionized water at 20-80 ° C until the final pH value is lower than 10; c) the wet material after washing is dried at 60-150 ° C for 6-60 h.
  • the step 3) in the method comprises: uniformly mixing the washed and dried precursor material with lithium hydroxide, calcining in an oxygen atmosphere furnace at 650 to 850 ° C for 10 to 30 hours, and cooling to After the room temperature, a ladder aluminum type lithium nickel cobalt aluminum oxide cathode material was obtained.
  • the invention aims at the problem of easy hydrolysis of Al 3+ , and proposes that the complex solution of aluminum alone is used as the aluminum source, and the aluminum source solution is gradually added to the intermediate solution (ie, the solution containing the complexing agent I) so that the aluminum in the mixed solution is made.
  • the concentration gradually increases, and the mixed solution in which the aluminum concentration is gradually increased, the nickel-cobalt salt solution, the sodium hydroxide solution, and the complexing agent solution are continuously added to the continuous reaction in the kettle, so that the aluminum element in the precursor has a spherical core to the spherical surface. Gradient distribution.
  • the concentration of the doped aluminum element continuously increases from the core to the spherical surface, and the surface aluminum content can even reach 100%.
  • the concentration of LiNi 1-xy Co x Al y O 2 doped with such a precursor increases continuously from the core to the spherical surface, and the surface aluminum content can even reach 100%, which not only improves the diffusion performance of lithium ions in the material body. It also fundamentally solves the material's stability in air and electrolyte, and can reduce the amount of aluminum to increase the energy density of the material.
  • a series of nickel-based gradient aluminum-doped composite materials were prepared by the method of the invention: LiNi 0.815 Co 0.15 Al 0.035 O 2 , LiNi 0.85 Co 0.10 Al 0.05 O 2 and LiNi 0.87 Co 0.10 Al 0.03 O 2 , etc.
  • the materials all exhibit high energy density, high safety stability and superior processing properties.
  • the method for preparing a spherical nickel hydroxide cobalt aluminum precursor material by the coprecipitation method and the preparation method of the lithium aluminum cobalt aluminum oxide cathode material for the ladder aluminum type lithium ion battery provided by the invention have a plurality of beneficial technical effects: (1) The gradient spherical nickel hydroxide cobalt aluminum precursor material prepared by the method of the invention and the positive electrode material, the concentration of aluminum gradually increases from the core to the particle surface in the radial direction, and the concentration at the outermost surface is the largest, possibly as high as 100%; (2) The method of the present invention can realize the preparation of a precursor which uniformly increases the surface aluminum element with the spherical nickel hydroxide cobalt aluminum particle center as a starting point by strictly controlling the system conditions; (3) prepared by the method of the present invention.
  • the gradient spherical nickel hydroxide cobalt aluminum precursor material and the positive electrode material have significantly improved moisture resistance, effectively avoiding the decomposition of trivalent nickel, and greatly reducing the humidity sensitivity in the preparation and application of the material, which is beneficial to the manufacture of NCA materials and related batteries.
  • some embodiments of the present invention also add a NaCl desulfurization washing step, which is effective in reducing the precursor.
  • the loss of elements increases the removal of harmful impurities, which is beneficial for the preparation of high stability lithium nickel cobalt cobalt aluminate.
  • Lithium positive electrode material Lithium positive electrode material; (5)
  • the positive electrode material of lithium nickel cobalt aluminate battery prepared by the method has stable electrochemical performance, high energy density, good rate performance, high safety, low sensitivity to temperature and humidity, and excellent processing performance. Such characteristics can be used to prepare power batteries that meet the needs of electronic products and electric vehicles; (6) By controlling the sintering process, it is possible to construct a gradient type nickel-cobalt lithium aluminate cathode material with a high stability surface, thus, the synthesized product High purity, good crystallization, excellent processing performance and good electrochemical performance; (7)
  • the method of the invention is simple and easy, the conditions are easy to control, and the green is highly efficient.
  • FIG. 1 is a schematic view showing the manner of feeding each raw material in the synthesis method of the present invention.
  • Example 2 is an SEM image of a precursor prepared in Example 1.
  • Example 3 is an XRD comparison diagram of the ladder aluminum precursor and the conventional coprecipitation precursor in Example 1.
  • Example 4 is a cycle performance curve of the positive electrode material prepared in Example 1.
  • Figure 5 is an SEM image of the precursor prepared in Example 2.
  • 6 is a comparison chart of charge and discharge curves (at 6a, 0.2C and 1C magnification) and a comparison of cycle performance curves (6b) of the positive electrode material prepared in Example 2 and ordinary NCA materials.
  • the nickel cobalt salt aqueous solution (20 ml/min), 30% sodium hydroxide solution (10 ⁇ 2 mL/min) and 14 mol/L ammonia aqueous solution (4 ⁇ 1 mL/min) to the reaction kettle, and biasing
  • the sodium aluminate solution was firstly fed at a flow rate of 1.45 ml/min to a continuously stirred mixing vessel containing a solution of the complexing agent I having a volume of 41.74 L, and the mixed solution was fed at a flow rate of 20 ml/min.
  • the reaction temperature in the reaction vessel is 50 ° C;
  • the concentration of the aluminum element in the mixing container is higher and higher, thereby feeding the reaction.
  • the concentration of aluminum in the mixed solution in the autoclave is also getting higher and higher, and the concentration of aluminum element in contact with the surface of the precipitated particles is also increased, and finally the ladder aluminum type which is distributed along the radial interface of the precipitated particles is obtained.
  • Nickel hydroxide cobalt aluminum precursor material since the volume of the solution containing the complexing agent I in the mixing container is continuously decreased, and the sodium metaaluminate solution is continuously added, the concentration of the aluminum element in the mixing container is higher and higher, thereby feeding the reaction.
  • the concentration of aluminum in the mixed solution in the autoclave is also getting higher and higher, and the concentration of aluminum element in contact with the surface of the precipitated particles is also increased, and finally the ladder aluminum type which is distributed along the radial interface of the precipitated particles is obtained.
  • the concentration of the complexing agent, the pH value and the particle size distribution were strictly controlled, and the reaction was stopped after the nickel-cobalt salt aqueous solution was added.
  • the mother liquor was filtered and washed with a 60 ° C, 10% sodium chloride solution for 30 min.
  • the slurry was washed, filtered, and dried to obtain Ni 0.815 Co 0.15 Al 0.035 with a surface aluminum concentration of 30 at% (
  • the precursor of OH) 2 see Fig. 2 for its SEM image) can be seen from the SEM image.
  • the morphology of the precursor is spherical or spheroidal, and the particle size distribution is concentrated.
  • the Ni 0.815 Co 0.15 Al 0.035 (OH) 2 was uniformly mixed with the metered lithium hydroxide, and then calcined in an oxygen atmosphere furnace at 750 ° C for 12 h to cool to room temperature to obtain a positive electrode material LiNi 0.815 Co 0.15 Al 0.035 O 2 , XRD.
  • the material was tested to have a single alpha-NaFeO 3 structure (see Figure 3).
  • the positive electrode material had a first discharge capacity of 198 mAh/g at a charge and discharge of 2.8 to 4.3 voltage window of 0.1 C, a discharge specific capacity of 174 mAh/g at 1 C, and a capacity retention rate of >82% at a cycle of 300 cycles (shown in Fig. 4).
  • the nickel cobalt salt aqueous solution (20 ml/min), 30% sodium hydroxide solution (10 ⁇ 2 mL/min) and 1 mol/L EDTA solution (3 ⁇ 1 mL/min) were added to the reaction kettle, and Al was added.
  • the -EDTA complex solution was first added to a continuously stirred mixing vessel containing a solution of the complexing agent I having a volume of 42.36 L at a flow rate of 1.05 ml/min, while the mixed solution was flowed at a flow rate of 20 ml/min.
  • the reaction temperature in the reactor is 50 ° C
  • the stirring speed is 400r / min;
  • the concentration of the complexing agent, the pH value and the particle size distribution were strictly controlled, and the reaction was stopped after the nickel-cobalt salt aqueous solution was added.
  • the mother liquor was filtered and washed with 60 ° C and 10% sodium chloride solution for 30 min.
  • the slurry was washed, filtered and dried to obtain Ni 0.80 Co 0.15 Al 0.05 with a surface aluminum concentration of 50 at% ( The precursor of OH) 2 (see Fig. 5 for its SEM image) can be seen from the SEM image.
  • the morphology of the precursor is spherical or spheroidal, and the particle size distribution is concentrated.
  • Ni 0.80 Co 0.15 Al 0.05 (OH) 2 was uniformly mixed with the metered amount of lithium hydroxide, and then calcined at 750 ° C for 12 hours in an oxygen atmosphere furnace to be cooled to room temperature to obtain a positive electrode material LiNi 0.8 Co 0.15 Al 0.05 O 2 .
  • the positive electrode material has a first discharge capacity of 188 mAh/g at a charge and discharge of 2.8 to 4.3 voltage window of 0.2 C, and a specific discharge capacity of 178 mAh/g at 1 C, and the cycle performance is significantly better than that of ordinary NCA materials (see Fig. 6).

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Abstract

一种制备具有铝元素梯度分布的镍钴铝前驱材料和正极材料的方法。所述方法所制备的前驱材料和基于所述前驱材料的正极材料为铝元素分布呈梯度变化的球形或类球形，粒度分布均匀。所合成的材料振实密度高，对环境二氧化碳和水分不敏感，加工性能好，比容量高，稳定特性好。

Description

制备具有铝元素梯度分布的镍钴铝前驱材料和正极材料的方法 技术领域
本发明涉及锂离子电池制造领域，具体地涉及制备具有铝元素梯度分布的镍钴铝前驱材料和正极材料的方法。
背景技术
目前，锂离子电池已经广泛地用于各种移动式电子产品和电动工具领域中，而正极材料是锂离子电池中提高能量密度、安全性以及降低成本的关键。进一步提高材料的功率密度、能量密度和改善安全性能是当今锂离子电池正极材料的发展方向。
在LiCoO2的诸多替代候选材料中，LiNiO2因其高容量、低成本、少污染而受到人们的关注；而LiNi1-xCoxO2除了具有LiNiO2高比容量、低成本的优势之外，还具有较好的循环性能，LiNi1-xCoxO2能发挥出190mAh/g的比容量，但是镍钴二元材料的稳定性仍然达不到现阶段3C(家电、计算机、通讯)电子产品和动力电池对材料的要求。
体相掺杂和表面包覆是改善镍系材料稳定性的最主要方法。以镍钴铝材料为代表的掺铝材料，LiNi1-x-yCoxAlyO2作为LiNiO2、LiCoO2和LiAlO2三者的类质同像固溶体，同时具备了能量密度高，热稳定性好，价廉环保等优点，已经成为3C领域和动力电池领域的高端储能材料。但是，由于三价镍的热力学不稳定性，致使NCA(镍钴铝酸锂材料)合成困难，二价镍离子难以氧化成三价，需要在纯氧气气氛下才能氧化完全。此外，由于NCA吸水性强，存在下式中的反应，电池生产需要在10％湿度以下条件才能正常生产。由于NCA容易放出O2，CO2等，电池容易气胀，最好采用18650型圆柱电池生产。
LiNi1-x-yCoxAlyO2+H2O→Ni1-x-yCoxAlyO+LiOH+O2
LiOH+CO2→Li2CO3
Li2CO3+HF→LiF+CO2
鉴于该材料本身的结构特性导致制备结构稳定的NCA材料和镍钴铝锂电池的条件非常苛刻。目前，国内生产的镍钴铝锂正极材料仍然存在充放电过程中容量衰减较快、倍率性能不好和储存性能极差等缺陷。为此，为了迎合温和的生产工艺，制备性能优越的镍钴铝材料，有必要开发新型的镍钴铝前驱体。
在镍钴铝酸锂正极材料的制备过程中，因为受到煅烧制度的限制，Al3+离子在～750℃下很难与Ni-Co形成固溶体而很少用单独镍、钴、铝原料固相混合烧结的方法。目前普遍认为Ni1-x-yCoxAly(OH)2是制备高性能镍钴铝的最佳前驱体。共沉淀法是制备LiNiCoAlO2及其表面修饰的一种简单，实用的方法。Ni、Co和Al的共沉淀，关键是克服Al3+易水解单独沉淀，难与镍钴元素形成单一结构的前驱体，无法形成高密度球形镍钴铝材料。针对Al3+易水解问题，专利CN 103094546A和CN 103553152A提出了以单独配制铝的络合溶液为铝源，采用并流加料方式和镍钴盐溶液、氢氧化钠溶液和氨溶液通过控制结晶制备球形镍钴铝的方法。但是该方法存在如下问题：1、制备的镍钴铝前驱体中往往残留大量的硫酸根离子不易洗涤脱除；2、CN 103553152A的5％wt～15％wt氢氧化钠溶液陈化处理有利于硫的脱除，但是在洗涤过程中往往会导致表面铝元素的流失，造成制备的材料表面缺铝而对正极材料的储存性能、加工性能和电化学循环稳定性不利。提高铝的掺杂量可以提高材料的循环稳定性、安全性能及加工性能和储存性能，然而大量的轻金属元素铝的引入会导致材料本身真密度的降低，导致材料体积能量密度的降低，并且没有电活性的Al元素的引入必然导致材料本身能量密度的降低。所以，在较低的Al掺杂量的情况下制备出高能量密度、高稳定性、优良的储存性能和加工性能成为了一个研究热点。
韩国汉阳大学Yang-Kook Sun早在2008年就开发出了新型的梯度锂离子电池材料，该材料的内核是镍含量较高的镍钴锰三元材料，外面包覆层为镍含量逐渐降低而锰和钴含量逐渐升高的镍钴锰材料。这种特殊的正极材料表现出了高能量密度、长寿命和很好的安全性能。国内也有 不少文献和专利报道了掺杂元素(Ni、Co、Mn、Mg、Al、Ti、Zr等)梯度变化的锂离子电池正极材料的制备方法。其中CN 102214819 A、CN 103078109 A和CN 103715424 A等发明专利中均包含了共沉淀法制备Al元素梯度分布的氢氧化物前驱体。但是其方法均为铝盐溶液逐渐加入混合镍钴混合盐溶液中以控制镍钴铝混合盐溶液中铝浓度逐渐变化而制备具有铝元素梯度变化的氢氧化物前驱体。其所用的氨络合体系中，Al3+几乎不和氨络合，Al3+很容易水解单独形成胶体而达不到Al3+元素在镍钴锰氢氧化物中的梯度掺杂，不利于制备高密度球形梯度掺铝前驱体。
发明内容
本发明提供一种采用共沉淀法制备球形氢氧化镍钴铝前驱材料的方法，以及基于该方法的梯铝型锂离子电池锂镍钴铝氧正极材料的制备方法，以便克服和避免已有技术的缺点和不足，提供一种简单易行，条件易于控制，能够合成具有优良的电化学性能、优越的加工性能和储存性能的梯铝型锂离子电池锂镍钴铝氧正极材料的制备方法。
根据本发明的第一方面，提供一种采用共沉淀法制备球形氢氧化镍钴铝前驱材料的方法，所述方法包括以下步骤：
a)配制镍盐和钴盐混合的镍钴盐水溶液、含有络合剂I的溶液、含有络合剂II的溶液和氢氧化钠溶液，并将铝盐与络合剂I混合配制成含铝络合溶液；
b)在反应釜中预先加入含有所述络合剂II的底液；
c)将所述镍钴盐水溶液、所述含有络合剂I的溶液、所述含有络合剂II的溶液、所述含铝络合溶液和所述氢氧化钠溶液加入不断搅拌的所述反应釜中沉淀反应获得所述前驱材料，其中所述镍钴盐水溶液、所述含有络合剂II的溶液和所述氢氧化钠溶液各自以恒定流速流加加入所述反应釜中，所述含铝络合溶液和所述含有络合剂I的溶液以以下方式加入：将所述含铝络合溶液以恒定流速流加加入固定体积的所述含有络合剂I的溶液中与所述含有络合剂I的溶液混合，同时将所述含铝络合溶液与所述含有络合剂I的溶液的混合溶液以恒定流速流加加入所述反应釜，从而 使得所述混合溶液中铝浓度逐渐增加。
根据本发明的一实施方式，所述方法中所述镍盐为硫酸镍、氯化镍、醋酸镍和硝酸镍中的一种或几种。
根据本发明的一实施方式，所述方法中所述钴盐为硫酸钴、氯化钴、醋酸钴和硝酸钴中的一种或几种。
根据本发明的一实施方式，所述方法中所述的络合剂I为三乙醇胺、氟化铵、柠檬酸、草酸、乙二胺四乙酸钠和氢氧化钠中的一种或几种。
根据本发明的一实施方式，所述方法中所述的络合剂II为氨水、三乙醇胺、氟化铵、柠檬酸、草酸、乙二胺四乙酸钠中的一种或几种。
根据本发明的一实施方式，所述方法中所述的铝盐为硝酸铝、硫酸铝或醋酸铝中的一种或几种。
根据本发明的一实施方式，所述方法中所述镍钴盐水溶液中镍盐与钴盐的摩尔比为1-19，例如所述镍钴盐水溶液中镍盐与钴盐的摩尔比可以为1、2、3、4、5、6、7、8、9、10、11、12、13、14、15、16、17、18或19。
根据本发明的一实施方式，所述方法中所述镍钴盐水溶液中镍盐和钴盐的总浓度为0.2～2.5mol/L，例如所述镍钴盐水溶液中镍盐和钴盐的总浓度可以为0.2mol/L、0.4mol/L、0.6mol/L、0.8mol/L、1.0mol/L、1.2mol/L、1.4mol/L、1.6mol/L、1.8mol/L、2.0mol/L、2.2mol/L或2.5mol/L。
根据本发明的一实施方式，所述方法中所述氢氧化钠溶液的浓度为2～10mol/L，例如所述氢氧化钠溶液的浓度可以为2mol/L、3mol/L、4mol/L、5mol/L、6mol/L、7mol/L、8mol/L、9mol/L或10mol/L。
根据本发明的一实施方式，所述方法中所述含铝络合溶液中铝元素和所述络合剂I的摩尔比为1∶0.01～20.0，例如所述含铝络合溶液中铝元素和所述络合剂I的摩尔比可以为1∶0.01、1∶0.05、1∶0.1、1∶0.2、1∶0.3、1∶0.3、1∶0.4、1∶0.5、1∶0.6、1∶0.7、1∶0.8、1∶0.9、1∶1.0、1∶1.5、1∶2.0、1∶2.5、1∶3.0、1∶3.5、1∶4.0、1∶4.5、1∶5.0、1∶5.5、1∶6.0、1∶6.5、1∶7.0、1∶7.5、1∶8.0、1∶8.5、1∶9.0、1∶10.0、1∶11.0、1∶12.0、1∶13.0、1∶14.0、1∶15.0、1∶16.0、1∶17.0、1∶18.0、1∶19.0或20.0。
根据本发明的一实施方式，所述方法中所述底液中络合剂II的浓度为0.3～2mol/L，例如所述底液中络合剂II的浓度可以为0.3mol/L、0.4mol/L、0.5mol/L、0.6mol/L、0.7mol/L、0.8mol/L、0.9mol/L、1.0mol/L、1.1mol/L、1.2mol/L、1.3mol/L、1.4mol/L、1.5mol/L、1.6mol/L、1.7mol/L、1.8mol/L、1.9mol/L或2.0mol/L。
根据本发明的一实施方式，所述方法中所述底液的pH为10～12，例如所述底液的pH可以为10、10.2、10.4、10.6、10.8、11、11.2、11.4、11.6、11.8或12。
根据本发明的一实施方式，所述方法中所述镍钴盐水溶液、所述含有络合剂II的溶液、所述氢氧化钠溶液和所述混合溶液流加加入所述反应釜的流速比为1∶(0.05～50)∶(0.1～10)∶(0.01～100)。
根据本发明的一实施方式，所述方法中所述含铝络合溶液流加加入固定体积的所述含有络合剂I的溶液中的流速为0.1mL/min～2000mL/min。
根据本发明的一实施方式，所述方法中所述反应釜中的搅拌速度为50～1000转/分钟。
根据本发明的一实施方式，所述方法中所述步骤c)中的反应温度为20～80℃。
根据本发明的一实施方式，所述方法中所述步骤c)中的反应时间为5至100小时。
根据本发明的第二方面，提供了一种梯铝型锂离子电池锂镍钴铝氧正极材料的制备方法，所述方法包括：
1)采用如第一方面中所述的方法制备球形氢氧化镍钴铝前驱材料；
2)将步骤1)获得的所述前驱材料洗涤、过滤和干燥；
3)将所述前驱材料与氢氧化锂均匀混合后，置于氧气气氛炉中煅烧，冷却至室温后获得所述梯铝型锂离子电池复合正极材料。
根据本发明的一实施方式，所述方法中所述步骤2)包括：将所述前驱材料用20～80℃、浓度为3～30wt％的氯化钠溶液搅拌清洗10～60min；b)采用20～80℃的去离子水清洗沉淀数次，至最终pH值低于10；c)将清洗后的湿料置于于60～150℃下干燥6～60h。
根据本发明的一实施方式，所述方法中所述步骤3)包括：将清洗干燥后的前驱材料与氢氧化锂均匀混合，于氧气气氛炉中于650～850℃煅烧10～30h，冷却至室温后获得梯铝型锂镍钴铝氧正极材料。
本发明针对Al3+易水解问题，提出了以单独配制铝的络合溶液为铝源，铝源溶液逐渐加入中间溶液(即含有络合剂I的溶液)中使得混合后的溶液中铝的浓度逐渐增加，将铝浓度逐渐增加的混合溶液、镍钴盐溶液、氢氧化钠溶液和络合剂溶液并流加入方应釜中连续反应，从而使前驱体中铝元素从球心到球面具有梯度分布。该方法制备的球形镍钴铝材料中，掺杂铝元素的浓度从核心到球面连续增加，表面铝含量甚至可以达到100％。这样的前驱体制备出的LiNi1-x-yCoxAlyO2掺杂铝元素浓度从核心到球面连续增加，表面铝含量甚至可以达到100％，不仅改善了锂离子在材料本体里面的扩散性能，也从根本上解决了材料在空气中和电解液中的稳定性能，并且可以减少掺铝量以提高材料的能量密度。采用本发明的方法制备了一系列的镍基梯度掺铝复合材料：LiNi0.815Co0.15Al0.035O2、LiNi0.85Co0.10Al0.05O2和LiNi0.87Co0.10Al0.03O2等等，所制备的材料均表现出了高能量密度、高安全稳定性和优越的加工性能。
因此，本发明提供的采用共沉淀法制备球形氢氧化镍钴铝前驱材料的方法，以及基于该方法的梯铝型锂离子电池锂镍钴铝氧正极材料的制备方法具有多个有益技术效果：(1)采用本发明的方法制备的梯度型球形氢氧化镍钴铝前驱材料以及正极材料，铝的浓度按径向从核向颗粒表面逐渐增大，在最表面浓度最大，可能高达100％；(2)本发明的方法能够通过严格控制体系条件，实现以球形氢氧化镍钴铝颗粒球心为原点向表面铝元素的均匀增加的前驱体的制备；(3)采用本发明的方法制备的梯度型球形氢氧化镍钴铝前驱材料以及正极材料，防潮性能显著提高，有效避免三价镍的分解，材料的制备与应用中对湿度敏感性都大大降低，有利于NCA材料以及相关电池的制造；(4)与现有方法相比，本发明中的一些实施方式中还增加了NaCl脱硫洗涤步骤，在降低前驱体中有效元素的流失的同时提高有害杂质的脱除，利于制备高稳定性的锂镍钴铝酸 锂正极材料；(5)通过该方法制备得到的镍钴铝酸锂电池正极材料，具有电化学性能稳定、能量密度大、倍率性能好、安全性高、温度、湿度敏感性低、加工性能优良等特点，可以用来制备满足电子产品及电动汽车所需的动力电池；(6)通过控制烧结工艺，能够构建具有高稳定性表面的梯度型镍钴铝酸锂正极材料，因此，合成的产品纯度高，结晶完好，加工性能优良，电化学性能好；(7)本发明的方法简单易行，条件易于控制，绿色高效。
上述说明仅是本发明技术方案的概述，为了能够更清楚了解本发明的技术手段，而可依照说明书的内容予以实施，并且为了让本发明的上述和其它目的、特征和优点能够更明显易懂，以下特举本发明的具体实施方式。
附图说明
通过阅读下文优选实施方式的详细描述，各种其他的优点和益处对于本领域普通技术人员将变得清楚明了。附图仅用于示出优选实施方式的目的，而并不认为是对本发明的限制。在附图中：
图1为本发明的合成方法中各原料进料方式的示意图。
图2为实施例1中制备的前驱体SEM图。
图3为实施例1中梯铝前驱体和普通共沉淀前驱体的XRD对比图。
图4为实施例1中制备的正极材料的循环性能曲线。
图5为实施例2中制备的前驱体的SEM图。
图6为实施例2中制备的正极材料与普通NCA材料的充放电曲线(6a，0.2C和1C倍率下)对比图和循环性能曲线(6b)对比图。
具体实施方式
下面将更详细地描述本公开的示例性实施方式。虽然下文中显示了本公开的示例性实施方式，然而应当理解，可以以各种形式实现本公开而不应被这里阐述的实施方式所限制。相反，提供这些实施方式是为了能够更透彻地理解本公开，并且能够将本公开的范围完整的传达给本领域的技术人员。应当理解，本领域技术人员能够设想出尽管没有在本说明书中明确描述或者记 载、但是实现了本发明并且包含在本发明精神、原理与范围内的各种方法、组分以及含量。本说明书中引述的所有例子与条件性语言都是出于说明和教导的目的，以帮助读者理解发明人对现有技术做出贡献的原理与概念，并且应该被理解为不限于这些具体引述的例子与条件。此外，为了更清楚地说明，省略了对于已知方法、组分以及含量的详细描述，以不混淆本发明的描述。应理解，除非特别说明，此处描述的各实施方式中的特征可以互相组合。
实施例1：
制备Ni+Co离子浓度为2mol/L且Ni∶Co＝81.5∶15的镍钴盐水溶液45L、质量浓度32％的氢氧化钠溶液30L、浓度为14mol/L的氨水溶液(含络合剂II的溶液)20L、铝元素含量为1mol/L的偏铝酸钠溶液(铝和氢氧根的络合溶液)(铝络合溶液)3.26L，pH＝12的氢氧化钠溶液41.74L(含络合剂I的溶液)；
在150L反应釜中预先加入40L氨水，温度为50℃，(NH3·H2O+NH4 +)的浓度为1mol/L，pH为11.50±0.02的水溶液。其中，pH值由pH计检测，(NH3·H2O+NH4 +)浓度由化学滴定法检测并用浓氨水流加快慢来调整其浓度；
将所述镍钴盐水溶液(20ml/min)、30％的氢氧化钠溶液(10±2mL/min)和14mol/L的氨水溶液(4±1mL/min)流加加入反应釜中，而偏铝酸钠溶液首先以1.45ml/min的流速流加加入装有体积为41.74L的含络合剂I的溶液的持续搅拌混合容器中，同时将混合后的溶液以20ml/min的流速流加加入反应釜中(参见图1)，反应釜中的反应温度为50℃；
其中具体地，进料开始后，由于混合容器中含络合剂I的溶液体积不断减少，而偏铝酸钠溶液不断加入，混合容器中的铝元素浓度越来越高，从而进料至反应釜中的混合后的溶液中铝元素的浓度也越来越高，沉淀颗粒表面接触到的铝元素浓度也随之升高，最终获得沿着沉淀颗粒径向界面铝元素梯度分布的梯铝型氢氧化镍钴铝前驱材料。
过程中严格控制络合剂浓度、pH值和粒度分布，镍钴盐水溶液加料完后停止反应。料浆经过30min陈化后，过滤母液，并用60℃、10％的氯化钠溶液搅拌清洗30min，料浆经过洗涤、过滤、干燥后获得表面铝浓 度为30at％的Ni0.815Co0.15Al0.035(OH)2前驱体(其SEM图参见图2)，从SEM图中可以看出，前驱体形貌为球形或类球形，粒度分布集中。将该Ni0.815Co0.15Al0.035(OH)2与计量比的氢氧化锂均匀混合后，置于氧气气氛炉中750℃煅烧12h冷却至室温获得了正极材料LiNi0.815Co0.15Al0.035O2，XRD检测该材料具有单一α-NaFeO3结构(参见图3)。该正极材料在2.8～4.3电压窗口充放电0.1C下首次放电容量为198mAh/g，1C下放电比容量保持在174mAh/g，循环300周容量保持率＞82％(图4所示)。
实施例2
制备Ni+Co离子浓度为2mol/L且Ni∶Co＝80∶15的镍钴盐水溶液45L、质量浓度30％的氢氧化钠溶液30L、浓度为1mol/L的EDTA(乙二胺四乙酸钠)溶液(含络合剂II的溶液)10L、铝元素含量为2mol/L的Al-EDTA溶液(铝络合溶液)2.37L，浓度为0.02mol/L的EDTA溶液(含络合剂I的溶液)42.63L；
在150L反应釜中预先加入40LEDTA溶液，温度为50℃，EDTA的浓度为0.05mol/L，pH为11.20±0.02的水溶液。其中，pH值由pH计检测，EDTA浓度由化学滴定法检测并用含络合剂II的溶液流加快慢来调整其浓度；
将所述镍钴盐水溶液(20ml/min)、30％的氢氧化钠溶液(10±2mL/min)和1mol/L的EDTA溶液(3±1mL/min)流加加入反应釜中，而Al-EDTA络合溶液首先以1.05ml/min的流速流加加入装有体积为42.36L的含络合剂I的溶液的持续搅拌混合容器中，同时将混合后的溶液以20ml/min的流速流加加入反应釜中(参见图1)，反应釜中的反应温度为50℃，搅拌速度为400r/min；
过程中严格控制络合剂浓度、pH值和粒度分布，镍钴盐水溶液加料完后停止反应。料浆经过30min陈化后，过滤母液，并用60℃、10％的氯化钠溶液搅拌清洗30min，料浆经过洗涤、过滤、干燥后获得表面铝浓度为50at％的Ni0.80Co0.15Al0.05(OH)2前驱体(其SEM图参见图5)，从SEM图中可以看出，前驱体形貌为球形或类球形，粒度分布集中。将Ni0.80Co0.15Al0.05(OH)2与计量比的氢氧化锂均匀混合后，置于氧气气氛炉 中750℃煅烧12h冷却至室温获得了正极材料LiNi0.8Co0.15Al0.05O2。该正极材料在2.8～4.3电压窗口充放电0.2C下首次放电容量为188mAh/g，1C下放电比容量保持在178mAh/g，循环性能明显优于普通NCA材料(参见图6)。
应当注意，上述实施方式对本发明进行说明而不是对本发明进行限制，并且本领域技术人员在不偏离所附权利要求的范围的情况下，可设计出各种替代实施方式。所属技术领域的技术人员应该明了，对本发明的任何改进，对本发明所选用组分的等效替换以及辅助组分的增加、具体方式的选择等，均落在本发明的保护范围和公开范围之内。

Claims (20)

  1. 一种采用共沉淀法制备球形氢氧化镍钴铝前驱材料的方法，其特征在于，所述方法包括以下步骤：
    a)配制镍盐和钴盐混合的镍钴盐水溶液、含有络合剂I的溶液、含有络合剂II的溶液和氢氧化钠溶液，并将铝盐与络合剂I混合配制成含铝络合溶液；
    b)在反应釜中预先加入含有所述络合剂II的底液；
    c)将所述镍钴盐水溶液、所述含有络合剂I的溶液、所述含有络合剂II的溶液、所述含铝络合溶液和所述氢氧化钠溶液加入不断搅拌的所述反应釜中沉淀反应获得所述前驱材料，其中所述镍钴盐水溶液、所述含有络合剂II的溶液和所述氢氧化钠溶液各自以恒定流速流加加入所述反应釜中，所述含铝络合溶液和所述含有络合剂I的溶液以以下方式加入：将所述含铝络合溶液以恒定流速流加加入固定体积的所述含有络合剂I的溶液中与所述含有络合剂I的溶液混合，同时将所述含铝络合溶液与所述含有络合剂I的溶液的混合溶液以恒定流速流加加入所述反应釜，从而使得所述混合溶液中铝浓度逐渐增加。
  2. 根据权利要求1所述的方法，其特征在于：所述镍盐为硫酸镍、氯化镍、醋酸镍和硝酸镍中的一种或几种。
  3. 根据权利要求1所述的方法，其特征在于：所述钴盐为硫酸钴、氯化钴、醋酸钴和硝酸钴中的一种或几种。
  4. 根据权利要求1所述的方法，其特征在于：所述的络合剂I为三乙醇胺、氟化铵、柠檬酸、草酸、乙二胺四乙酸钠和氢氧化钠中的一种或几种。
  5. 根据权利要求1所述的方法，其特征在于：所述的络合剂II为氨水、三乙醇胺、氟化铵、柠檬酸、草酸、乙二胺四乙酸钠中的一种或几种。
  6. 根据权利要求1所述的方法，其特征在于：所述的铝盐为硝酸铝、硫酸铝或醋酸铝中的一种或几种。
  7. 根据权利要求1所述的方法，其特征在于：所述镍钴盐水溶液中镍盐与钴盐的摩尔比为1-19。
  8. 根据权利要求1所述的方法，其特征在于：所述镍钴盐水溶液中镍盐和钴盐的总浓度为0.2～2.5mol/L。
  9. 根据权利要求1所述的方法，其特征在于：所述氢氧化钠溶液的浓度为2～10mol/L。
  10. 根据权利要求1所述的方法，其特征在于：所述含铝络合溶液中铝元素和所述络合剂I的摩尔比为1∶0.01～20.0。
  11. 根据权利要求1所述的方法，其特征在于：所述底液中络合剂II的浓度为0.3～2mol/L。
  12. 根据权利要求1所述的方法，其特征在于：所述底液的pH为10～12。
  13. 根据权利要求1所述的方法，其特征在于：所述镍钴盐水溶液、所述含有络合剂II的溶液、所述氢氧化钠溶液和所述混合溶液流加加入所述反应釜的流速比为1∶(0.05～50)∶(0.1～10)∶(0.01～100)。
  14. 根据权利要求1所述的方法，其特征在于：所述含铝络合溶液流加加入固定体积的所述含有络合剂I的溶液中的流速为0.1mL/min～2000mL/min。
  15. 根据权利要求1所述的方法，其特征在于：所述反应釜中的搅拌速度为50～1000转/分钟。
  16. 根据权利要求1所述的方法，其特征在于：所述步骤c)中的反应温度为20～80℃。
  17. 根据权利要求1所述的方法，其特征在于：所述步骤c)中的反应时间为5至100小时。
  18. 一种梯铝型锂离子电池锂镍钴铝氧正极材料的制备方法，其特征在于，所述方法包括：
    1)采用如权利要求1-17所述的方法制备球形氢氧化镍钴铝前驱材料；
    2)将步骤1)获得的所述前驱材料洗涤、过滤和干燥；
    3)将所述前驱材料与氢氧化锂均匀混合后，置于氧气气氛炉中煅烧，冷却至室温后获得所述梯铝型锂离子电池复合正极材料。
  19. 根据权利要求17所述的方法，其特征在于：所述步骤2)包括：将所述前驱材料用20～80℃、浓度为3～30wt％的氯化钠溶液搅拌清洗10～60min；b)采用20～80℃的去离子水清洗沉淀数次，至最终pH值低于10；c)将清洗后的湿料置于于60～150℃下干燥6～60h。
  20. 根据权利要求18或19所述的方法，其特征在于：所述步骤3)包括：将清洗干燥后的前驱材料与氢氧化锂均匀混合，于氧气气氛炉中于650～850℃煅烧10～30h，冷却至室温后获得梯铝型锂镍钴铝氧正极材料。
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