阅读说明：本技术 正极活性材料、正极极片及锂离子二次电池 (Positive electrode active material, positive electrode plate and lithium ion secondary battery ) 是由 钭舒适 胡春华 蒋耀 吴奇 何金华 邓斌 于 2019-09-02 设计创作，主要内容包括：本发明公开了一种正极活性材料、正极极片及锂离子二次电池。正极活性材料包括含镍的锂复合氧化物,含镍的锂复合氧化物的分子式为Li_(1+a)[Ni_xCo_yMn_zM_b]O_2,分子式中,M为过渡金属位掺杂元素,0.5≤x<1,0≤y<0.3,0≤z<0.3,-0.1≤a<0.2,0<b<0.3,x+y+z+b＝1；正极活性材料具有层状晶体结构,属于空间群；正极活性材料在78％脱锂态时,至少部分掺杂元素M的化合价为+3价以上、且正极活性材料的表面氧平均价态V_O为-2.0≤V_O≤-1.5。采用本发明提供的正极活性材料,能够使锂离子二次电池同时兼顾较高的能量密度及高温循环性能。(The invention discloses a positive active material, a positive pole piece and a lithium ion secondary battery. The positive electrode active material includes a nickel-containing lithium composite oxide having a molecular formula of Li 1+a [Ni x Co y Mn z M b ]O 2 In the molecular formula, M is a transition metal site doping element, x is more than or equal to 0.5<1，0≤y<0.3，0≤z<0.3，‑0.1≤a<0.2，0<b<0.3, x + y + z + b ═ 1; the positive electrode active material has a layered crystal structure A space group; when the positive electrode active material is in a 78% delithiated state, the valence of at least part of the doping element M is more than +3, and the surface oxygen average valence V of the positive electrode active material O V is-2.0 or less O Less than or equal to-1.5. The positive active material provided by the invention can enable the lithium ion secondary battery to have higher energy density and high-temperature cycle performance at the same time.)

1. A positive electrode active material characterized in that,

the positive electrode active material includes a nickel-containing lithium composite oxide having a molecular formula of Li_1+a[Ni_xCo_yMn_zM_b]O₂In the molecular formula, M is a transition metal site doping element, and x is more than or equal to 0.5<1，0≤y<0.3，0≤z<0.3，-0.1≤a<0.2，0<b<0.3，x+y+z+b＝1；

The positive active material has a layered crystal structure and belongs to the R3m space group;

when the positive electrode active material is in a 78% delithiated state, the valence of at least part of the doping element M is more than +3, and the surface oxygen average valence V of the positive electrode active material_OV is-2.0 or less_O≤-1.5。

2. The positive electrode active material according to claim 1, comprising secondary particles in which the primary particles are aggregated, wherein the mass concentration of the doping element M at any point in the secondary particles is not more than 20%.

3. The positive electrode active material according to claim 1 or 2, wherein the positive electrode active material has a bulk-structure oxygen defect formation energy Δ Ε in a 78% delithiated state_O-vacSatisfies the following conditions: delta E_O-vacNot less than 0.5eV, preferred Δ E_O-vac≥0.7eV。

4. The positive electrode active material according to any one of claims 1 to 3, wherein the doping element M has two or more different valence states in a 78% delithiated state, and the valence of the doping element M at the highest valence state is one or more of +4 valence, +5 valence, +6 valence, +7 valence, and +8 valence states;

preferably, the doping element M includes one or more of Ti, V, Se, Zr, Nb, Ru, Pd, Sb, Te and W.

5. The positive electrode active material according to any one of claims 1 to 4, wherein the positive electrode active material has a true density ρ_TrueIs 4.6g/cm³≤ρ_True≤4.9g/cm³。

6. The positive electrode active material according to any one of claims 1 to 5, wherein the true doping concentration ω of the positive electrode active material is 2300 μ g/cm³≤ω≤49100μg/cm³Preferably 3000. mu.g/cm³≤ω≤30000μg/cm³。

7. The positive electrode active material according to any one of claims 1 to 6, wherein a deviation ε between a mass concentration of the doping element M in the positive electrode active material and an average mass concentration of the doping element M in the particles of the positive electrode active material is 30% or less, preferably 20% or less.

8. The positive electrode active material according to any one of claims 1 to 7,

the average particle diameter D of the positive electrode active material_v50 is 5 to 20 μm, preferably 8 to 15 μm, and more preferably 9 to 11 μm; and/or the presence of a gas in the gas,

the specific surface area of the positive electrode active material was 0.2m²/g～1.5m²A/g, preferably of 0.3m²/g～1m²(ii)/g; and/or the presence of a gas in the gas,

the tap density of the positive electrode active material is 2.3g/cm³～2.8g/cm³(ii) a And/or the presence of a gas in the gas,

the positive electrode active material has a compacted density of 3.1g/cm at a pressure of 5 tons³～3.8g/cm³。

9. The positive electrode active material according to any one of claims 1 to 8, wherein in the formula, 0.7. ltoreq. x.ltoreq.0.9, 0< y <0.3, 0< z < 0.3;

the surface oxygen average valence V of the anode active material in 78% delithiation state_OV is more than or equal to-1.9_O≤-1.6。

10. A positive electrode sheet comprising a positive electrode current collector and a positive electrode active material layer provided on the positive electrode current collector, wherein the positive electrode active material layer comprises the positive electrode active material according to any one of claims 1 to 9.

11. A lithium ion secondary battery comprising the positive electrode sheet according to claim 10.

Technical Field

The invention belongs to the technical field of secondary batteries, and particularly relates to a positive active material, a positive pole piece and a lithium ion secondary battery.

Background

A lithium ion secondary battery is a rechargeable battery that mainly operates by movement of lithium ions between a positive electrode and a negative electrode, and is a clean energy source that is currently widely used. The positive electrode active material is used as an important component of the lithium ion secondary battery and provides lithium ions which move in a reciprocating manner between the positive electrode and the negative electrode in the charging and discharging process of the battery, so that the positive electrode active material is very important for the performance of the battery.

The lithium nickel-based positive electrode active material has higher theoretical capacity, and a lithium ion secondary battery adopting the lithium nickel-based positive electrode active material can expect to obtain higher energy density, but researches find that the high-temperature cycle performance of the lithium ion secondary battery is poorer.

Disclosure of Invention

The embodiment of the invention provides a positive active material, a positive pole piece and a lithium ion secondary battery, aiming at ensuring that the lithium ion secondary battery has higher energy density and high-temperature cycle performance at the same time.

In one aspect, the present invention provides a positive electrode active material including a nickel-containing lithium composite oxide having a molecular formula of Li_1+a[Ni_xCo_yMn_zM_b]O₂In the molecular formula, M is a transition metal site doping element, x is more than or equal to 0.5<1，0≤y<0.3，0≤z<0.3，-0.1≤a<0.2，0<b<0.3, x + y + z + b ═ 1; the positive electrode active material has a layered crystal structureA space group; when the positive electrode active material is in a 78% delithiated state, the valence of at least part of the doping element M is more than +3, and the surface oxygen average valence V of the positive electrode active material_OV is-2.0 or less_O≤-1.5。

A second aspect of embodiments of the present invention provides a positive electrode sheet, including a positive electrode current collector and a positive electrode active material layer disposed on the positive electrode current collector, where the positive electrode active material layer includes the positive electrode active material according to the first aspect of the present invention.

A third aspect of embodiments of the present invention provides a lithium ion secondary battery comprising a positive electrode sheet according to the second aspect of the present invention.

Compared with the prior art, the embodiment of the invention at least has the following beneficial effects:

the positive active material provided by the embodiment of the invention comprises the nickel-containing lithium composite oxide with a specific chemical composition and structure, so that the positive active material has higher charge-discharge voltage and specific capacity characteristics, and a lithium ion secondary battery adopting the positive active material can show higher capacity performance and energy density. The positive active material also comprises a doping element M, and when the positive active material is in a 78% delithiation state, the valence of at least part of the doping element M is more than +3 valence. Through M element doping modification, the difference between the surface oxygen valence Vo of the anode active material in a 78% delithiation state and the ground state oxygen valence (-2 valence) is in a smaller range, the structural stability of the anode active material can be obviously improved, surface side reactions are reduced, and the high-temperature cycle performance of the battery is obviously improved. Therefore, the positive electrode active material of the embodiment of the invention ensures that the lithium ion secondary battery has higher energy density and high-temperature cycle performance at the same time.

Drawings

In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings needed to be used in the embodiments of the present invention will be briefly described below, and it is obvious that the drawings described below are only some embodiments of the present invention, and it is obvious for those skilled in the art that other drawings can be obtained according to the drawings without creative efforts.

FIG. 1 is a distribution image of doping elements of secondary particles of a positive electrode active material according to example 1, which is obtained by preparing a Cross Section using an IB-09010CP type Cross Section Polisher (CP) of Japanese Electron (JEOL) corporation and testing the Cross Section using an Oxford instrument X-Max type Energy spectrometer (EDS); the bright spots in the figure indicate the doping elements, which are uniformly distributed in the particles.

Fig. 2 is a schematic view of dot positions in a mass concentration deviation test of a doping element in secondary particles of positive electrode active materials of examples 1 to 25 and comparative examples 1 to 4.

Fig. 3 is an X-ray photoelectron spectroscopy (XPS) spectrum of the Sb 3d orbital in a 78% delithiated state of the positive electrode active material of example 1.

Fig. 4 is an XPS spectrum of the O1s orbital in 78% delithiated state of the positive electrode active material of example 1.

Detailed Description

In order to make the objects, technical solutions and advantageous technical effects of the present invention more clear, the present invention is further described in detail with reference to the following embodiments. It should be understood that the embodiments described in this specification are only for the purpose of explaining the present invention and are not intended to limit the present invention.

For the sake of brevity, only some numerical ranges are explicitly disclosed herein. However, any lower limit may be combined with any upper limit to form ranges not explicitly recited; and any lower limit may be combined with any other lower limit to form a range not explicitly recited, and similarly any upper limit may be combined with any other upper limit to form a range not explicitly recited. Also, although not explicitly recited, each point or individual value between endpoints of a range is encompassed within the range. Thus, each point or individual value can form a range not explicitly recited as its own lower or upper limit in combination with any other point or individual value or in combination with other lower or upper limits.

In the description herein, it is to be noted that, unless otherwise specified, "above" and "below" are inclusive, and "a plurality" of "one or more" means two or more, "and" a plurality "of" one or more "means two or more.

The above summary of the present invention is not intended to describe each disclosed embodiment or every implementation of the present invention. The following description more particularly exemplifies illustrative embodiments. At various points throughout this application, guidance is provided through a list of embodiments that can be used in various combinations. In each instance, the list is merely a representative group and should not be construed as exhaustive.

Positive electrode active material

First, a positive electrode active material according to a first aspect of an embodiment of the present invention will be described. The positive electrode active material includes a nickel-containing lithium composite oxide having a molecular formula of Li_1+a[Ni_xCo_yMn_zM_b]O₂Wherein M is a transition metal site doping element, x is more than or equal to 0.5<1，0≤y<0.3，0≤z<0.3，-0.1≤a<0.2，0<b<0.3, x + y + z + b ═ 1; the positive electrode active material has a layered crystal structureA space group; when the positive electrode active material is in a 78% delithiated state, the valence of at least part of the doping element M is more than +3, and the surface oxygen average valence V of the positive electrode active material_OV is-2.0 or less_O≤-1.5。

Herein, the "78% delithiated state" refers to a state in which the molar content of lithium extracted from the positive electrode active material during charging of the battery is 78% of the theoretical lithium content. In the actual use process of the secondary battery, a "full charge state" is generally set, and a "charge cut-off voltage" is correspondingly set so as to ensure the safe use of the battery. The "fully charged State" means that the State of Charge (SOC) of the secondary battery is 100%, in other words, the secondary battery having the positive electrode composition including the positive electrode active material described above is charged to the Charge cut-off voltage within the range in which reversible Charge and discharge are performed. The "fully charged state" or "charge cut-off voltage" may vary depending on the positive electrode active material or the safety requirement. When a secondary battery prepared by the nickel-containing lithium composite oxide positive active material is in a full charge state, the lithium removal state of the positive active material is about 78% lithium removal state generally so as to ensure normal use.

In this context, the correspondence between "delithiated state" and charging voltage is combined to conduct a study to obtain a positive electrode active material in "78% delithiated state". Specifically, a series of batteries using the positive electrode active material are charged to 2.8V, 2.9V, 3.0V, 3.1V, 3.2V, 3.3V, …, 4.0V, 4.1V, 4.2V, 4.3V, 4.4V, and 4.5V at a rate of 0.1C (i.e., the charging voltage interval is 0.1V), then positive electrode plates of the batteries are removed, the electrolyte is removed by washing, the positive electrode active material is digested, the mass concentrations of Li, transition metal, and O elements of the positive electrode active material are measured by an inductively coupled plasma-Emission spectrometer (ICP-OES), the stoichiometric ratio of each element of the positive electrode active material at the charging voltage is calculated, and the chemical formula of the positive electrode active material at the charging voltage is obtained, and further the charging voltage corresponding to "78% delithiation" is obtained.

And charging the battery containing the anode active material to be detected to the voltage corresponding to the 78% delithiation state, namely disassembling the battery to obtain the anode active material in the 78% delithiation state for further research. Surface oxygen valence state V of 78% delithiation state positive electrode active material_OAnd the valence of the doping element M can be obtained by X-ray photoelectron spectroscopy (XPS) test. More precisely, it can be obtained by Synchrotron radiation photoelectron spectroscopy (SRPES) test.

The positive active material of the embodiment of the invention comprises the nickel-containing lithium composite oxide with specific chemical composition and structure, so that the positive active material has higher charge-discharge voltage and specific capacity characteristics, and a lithium ion secondary battery adopting the positive active material can show higher capacity performance and energy density.

The surface oxygen valence of the non-delithiated positive active material is lower (such as-2 valence), and in the process of delithiating the positive active material (in the process of charging the battery), along with the deintercalation of lithium ions from the positive active material, electrons in the positive active material are also continuously deintercalated to reach the negative electrode. The positive active material also comprises a doping element M, and when the positive active material is in a 78% delithiation state, the valence of part or all of the doping element M is more than +3 valence. The doping element M with a larger valence can contribute more electrons in the positive active material, and the number of lost electrons of oxygen atoms of the corresponding positive active material is reduced, so that the surface oxygen activity of the positive active material in the lithium removal process and after lithium removal is always kept at a lower level, and particularly the surface oxygen average valence V of the positive active material in a 78% lithium removal state_OIs-2.0 to-1.5.

Through doping modification of the M element, the difference between the surface oxygen valence Vo of the anode active material in a 78% delithiation state and the ground state oxygen valence (-2 valence) is smaller, the structural stability of the anode active material can be obviously improved, the anode active material is not easy to generate an oxygen release phenomenon in the heating and temperature rise and high-temperature circulation process, oxygen defects are inhibited, the anode active material is effectively prevented from generating irreversible phase change, and the capacity retention rate of the anode active material in the high-temperature circulation process is improved. Therefore, the invention can obviously improve the high-temperature cycle performance of the battery by doping the M element at the transition metal position of the nickel-containing lithium composite oxide. In addition, the thermal stability and high-temperature safety performance of the battery are also improved.

The surface oxygen activity of the positive active material is low, the side reaction of the electrolyte on the surface of the material particles can be effectively inhibited, the gas generation is inhibited, the heat generation quantity is reduced, the consumption of reversible lithium ions is reduced, the impedance increase of the positive electrode is inhibited, the polarization of the positive electrode is reduced, and the high-temperature cycle performance of the battery is favorably improved.

By adopting the positive electrode active material provided by the embodiment of the invention, the lithium ion secondary battery can simultaneously give consideration to higher capacity performance, energy density and high-temperature cycle performance.

In some alternative embodiments, the nickel-containing lithium composite oxide may have a nickel content in the transition metal site element of 50 to 90 mol%, for example, 70 to 90 mol%. The high-nickel positive electrode active material has higher specific capacity characteristic, and can improve the capacity performance and energy density of the battery.

Furthermore, in the molecular formula of the nickel-containing lithium composite oxide, x is more than or equal to 0.7 and less than or equal to 0.9, and 0<y<0.3，0<z<0.3; and the surface oxygen average valence V of the anode active material in a 78% delithiation state_OV is more than or equal to-1.9_OLess than or equal to-1.6. The battery adopting the positive active material has higher energy density and high-temperature cycle performance.

The doping element M with the valence of more than +3 has strong binding capacity with oxygen, namely the bonding energy with oxygen is large, and oxygen atoms can be effectively bound, so that the oxygen release of the positive active material is not easy to occur in the heating and high-temperature circulation processes, and the oxygen defect formation energy delta E of the positive active material is improved_O-vac. In some embodiments, the positive electrode active material has a bulk structure oxygen defect formation energy Δ E in a 78% delithiated state_O-vacSatisfies Δ E_O-vacNot less than 0.5eV, and preferably satisfies Δ E_O-vac≥0.7eV。

Oxygen defect formation energy Δ E of positive electrode active material in "78% delithiation state" bulk structure_O-vacSatisfies the formula (1).

ΔE_O-vac＝E_pristine-E_defect-E_OFormula (1)

In the formula (1), Δ E_O-vacA bulk structure oxygen defect formation energy indicating that the positive electrode active material is in a "78% delithiation state" in a ground state; e_pristineBulk structural energy representing a "78% delithiated state" of the structurally intact positive electrode active material in the ground state; e_defectBulk structural energy representing a "78% delithiation state" of the positive electrode active material having an oxygen defect in a ground state; e_ORepresents the energy (chemical potential) of an oxygen atom in the ground state.

E_pristine、E_defectAnd E_OAll can be obtained by VASP calculation based on the first principle of the density functional theory, and the exchange correlation functional can adopt generalized gradient approximation (Genraliz)ed Gradient application, GGA) is added with a Hubbard parameter U corresponding item, namely GGA + U exchange correlation functional. As an example, the following steps may be included:

s10, obtaining information such as unit cell parameters and element occupation of the 78% delithiation state positive active material based on the X-ray diffraction (XRD) analysis result of the 78% delithiation state positive active material, and accordingly constructing a bulk phase structure model of the 78% delithiation state positive active material with a complete structure, wherein the structure of the model satisfies the requirement of the bulk phase structure model of the 78% delithiation state positive active materialUsing a computing software VASP based on a first principle of a density functional theory to exchange a correlation functional by adopting GGA + U, performing structure optimization on the model until the energy is converged, extracting the optimized structure energy, and recording the structure energy as E_pristine。

S20, deducting an oxygen atom on the basis of the optimized 78% delithiation state positive electrode active material bulk phase structure model to obtain a bulk phase model of the oxygen defect-containing positive electrode active material in the 78% delithiation state, exchanging a correlation functional by using a computing software VASP based on a first principle of a density functional theory, performing structure optimization on the oxygen defect-containing bulk phase model by using GGA + U to converge energy, extracting optimized structure energy, and recording the structure energy as E_defect。

S30, using computing software VASP based on the first principle of the density functional theory, exchanging the correlation functional by adopting GGA + U, optimizing oxygen molecules until energy convergence, extracting the optimized oxygen energy divided by 2, and marking as E_O。

S40, E obtained_pristine、E_defectAnd E_OThe numerical value of (2) is substituted for the formula (1), and the oxygen defect formation energy of one oxygen atom is calculated.

Subtracting different oxygen atoms with reference to step S20 to obtain defect formation energies of different oxygen atoms, and selecting the minimum value as the oxygen defect formation energy Delta E of the bulk structure of the positive electrode active material in "78% delithiation state_O-vac。

The calculation of the above steps S10, S20, S30The precision of the used calculation parameters ensures that the structure energy of the optimization calculation is converged to be less than 10^-6eV, force convergence to less thanThe calculation result can be ensured to be more reliable.

Oxygen defect formation energy Δ E of positive electrode active material in "78% delithiation state" bulk structure_O-vacWithin the above range, the oxygen atoms in the positive active material are not easy to separate from the original lattice position to form oxygen defects in the charging process and the fully charged state, so that the positive active material has high structural stability and is always kept in a lamellar phase state with strong electrochemical activity, a good carrier is provided for de-intercalation of lithium ions, the positive active material has high initial capacity and cycle capacity retention rate, and the energy density and high-temperature cycle performance of the battery are improved.

Bulk structure oxygen defect formation energy Δ E of positive electrode active material in "78% delithiation state_O-vacWithin the above range, the positive active material is not prone to oxygen release during heating and high-temperature cycling, and the thermal stability and high-temperature safety performance of the battery are improved.

In some preferred embodiments, in the positive active material in the 78% delithiated state, the doping element M has two or more different valence states, and the valence of the M element in the highest valence state is one or more of +4, +5, +6, +7, and + 8. The doping element M with higher valence and variable valence can contribute more electrons in the positive active material, and correspondingly, the number of lost electrons of oxygen atoms in the positive active material is less, so that the surface oxygen activity of the positive active material is further reduced, the material structure is stabilized, the surface side reaction is reduced, and the high-temperature cycle performance of the battery is further improved. In addition, the doping element with higher valence state has stronger binding capacity with oxygen, namely, the bonding energy of the doping element with higher valence state and oxygen is larger, so that oxygen atoms can be effectively bound, and the oxygen defect formation energy delta E of the anode active material is improved_O-vacAnd structural stability, thereby improving the performance of the battery.

In addition, when the positive active material is in a 78% delithiated state, the doping element M has more than two different valence states, wherein the lower valence state doping element can further contribute electrons to support the positive electrode to release more lithium ions, so that the energy density of the battery is further improved.

Further, the doping element M preferably includes one or more of Ti, V, Se, Zr, Nb, Ru, Pd, Sb, Te, and W, and can better exert the above effects and improve the energy density and high-temperature cycle performance of the lithium ion secondary battery.

In some preferred embodiments, the positive electrode active material includes secondary particles formed by aggregating the primary particles. Further, the variation in the mass concentration of the doping element at any one point in the secondary particles is 32% or less, preferably 30% or less, and more preferably 20% or less.

In this context, the mass concentration of the doping element at any one point in the secondary particle is the mass concentration of the doping element in all elements in the one-point minimum range, and can be obtained by EDX (Energy Dispersive X-Ray Spectroscopy) or EDS (EDS elemental analysis) in combination with TEM (Transmission Electron Microscope) or SEM (Scanning Electron Microscope) single-point Scanning test element concentration distribution or other similar manners. Wherein when EDX or EDS elemental analysis is combined with TEM or SEM single-point scanning test, the mass concentration of doping element in μ g/g at different sites in the secondary particles is respectively marked as η₁、η₂、η₃、…、η_nAnd n is a positive integer greater than 15.

The average mass concentration of the doping element in the secondary particles is the mass concentration of the doping element in all elements in the range of the single or multiple secondary particles, and can be obtained by EDX or EDS elemental analysis combined with TEM or SEM surface scan test of the element concentration distribution or other similar manners. Wherein the test surface includes all points in the single point test described above when tested in a manner that EDX or EDS elemental analysis combined with TEM or SEM surface scanning test element concentration distribution. The average mass concentration of the doping element in the secondary particles is recorded asThe unit is μ g/g.

The mass concentration deviation σ of the doping element at any point in the secondary particle can be calculated according to the formula (2):

the mass concentration deviation σ of the doping element at any one point in the secondary particles is 32% or less, preferably 30% or less, more preferably 20% or less, meaning that the distribution uniformity of the doping element in the secondary particles is high. The uniform doping can effectively reduce the surface oxygen activity of the positive active material and improve the formation energy of the bulk phase structure oxygen defects of the positive active material, thereby better improving the overall performance of the battery.

In addition, the properties of the uniformly doped positive active material particles are kept consistent, the migration and diffusion capacities of lithium ions in different areas in the particles are at the same level, the deformation resistance of the particles are close to each other, the stress distribution in the particles is uniform, the structural stability of the positive active material is improved, the positive active material is not easy to crack, the side reaction, the capacity and the cycle performance deterioration caused by the fresh surface exposed by cracking are prevented, the positive active material has high capacity exertion and high-temperature cycle capacity retention rate, and the battery has high capacity performance, energy density and high-temperature cycle performance.

The smaller the deviation of the mass concentration of the doping element at any point in the secondary particles is, the more uniform the distribution of the doping element in the particles is, and the more the structural stability of the positive electrode active material can be improved, and the capacity exertion and high-temperature cycle performance of the positive electrode active material can be improved.

In some preferred embodiments, the true doping concentration ω of the positive electrode active material is preferably 1500 μ g/cm³≤ω≤60000μg/cm³More preferably 2300. mu.g/cm³≤ω≤49100μg/cm³More preferably 3000. mu.g/cm³≤ω≤30000μg/cm³。

Herein, the true doping concentration ω of the positive electrode active material can be calculated from formula (3):

in the formula (3), ω is the true doping concentration of the positive electrode active material in μ g/cm³。

ρ_TrueIs the true density of the positive electrode active material and has the unit of g/cm³Which is equal to the ratio of the mass of the positive electrode active material to the true volume of the positive electrode active material, wherein the true volume is the actual volume of the solid substance, excluding the pores inside the particles. ρ true can be measured using instruments and methods known in the art, for example, gas volumetric methods, and can be performed using a powder true density tester.

Is the mass concentration of the doping element in units of μ g/g in the positive electrode active material, i.e., the mass of the doping element contained per gram of the positive electrode active material. Wherein the content of the first and second substances,represents the whole content of the doping elements in the macroscopic positive electrode active material, and comprises the doping elements doped in the particles of the positive electrode active material, the doping elements enriched in other phases on the surface of the positive electrode active material particles, and the doping elements positioned among the particles of the positive electrode active material.Can be obtained by measurement of absorption spectrum of positive electrode active material solution, such as ICP (inductively Coupled Plasma Emission Spectrometer), XAFS (X-ray absorption fine structure spectrum), and the like.

The real doping concentration of the positive active material is in the range, so that the surface oxygen activity of the positive active material can be effectively reduced, and the formation energy of bulk phase structure oxygen defects can be improved; the positive active material has a good layered crystal structure, so that the positive active material provides a good carrier for the de-intercalation of lithium ions, the intercalation and de-intercalation of the lithium ions are facilitated, the reversible lithium ions are prevented from being consumed on the surface of an electrode or in electrolyte, and the positive active material has high initial capacity and circulating capacity retention rate, so that the energy density and high-temperature circulating performance of the battery are improved.

In addition, the real doping concentration of the positive active material is in the range, doping elements are also ensured to be doped in the transition metal layer, the transition metal layer is prevented from entering the lithium layer, particles are ensured to have higher lithium ion transmission and diffusion capacity, and the battery has higher capacity exertion and cycle performance.

In some preferred embodiments, the mass concentration of the doping element in the positive electrode active materialAnd the average mass concentration of the doping element in the particles of the positive electrode active materialHas a deviation of epsilon, epsilon satisfies epsilon<50 percent. Preferably, ε ≦ 30%. More preferably, ε ≦ 20%.

Here, the particles of the positive electrode active material may include primary particles and/or secondary particles. Wherein the average mass concentration of the doping element in the primary particles, and the average mass concentration of the doping element in the primary particles and the secondary particles can be referred to the average mass concentration of the doping element in the secondary particles as described aboveAnd (6) carrying out testing.

Mass concentration of doping element in positive electrode active materialAnd the average mass concentration of the doping element in the particles of the positive electrode active materialThe deviation e of (d) can be calculated by the following equation (4):

it is understood that, when the particles of the positive electrode active material are secondary particles,

mass concentration of doping element in positive electrode active materialAnd the average mass concentration of the doping element in the particles of the positive electrode active materialThe deviation epsilon of the positive electrode active material is within the range, which means that the doping elements can be smoothly doped into the particles of the positive electrode active material, the contents of the doping elements distributed in other phases on the surfaces of the particles and the doping elements embedded among gaps of the particles are less, the macro and micro consistency of the positive electrode active material is better, the structure is uniform, the expansion and contraction degrees of each particle are kept consistent in the charge-discharge cycle process, the stability of the particles is high, and the positive electrode active material is beneficial to higher capacity exertion and high-temperature cycle performance.

In some preferred embodiments, the true density ρ of the positive electrode active material_TruePreferably 4.6g/cm³≤ρ_True≤4.9g/cm³This enables the positive electrode active material to have a higher specific capacity, thereby improving the capacity performance and energy density of the battery.

In the examples of the present invention, the average particle diameter D of the positive electrode active material particles_v50 is preferably 5 to 20 μm, more preferably 8 to 15 μm, and still more preferably 9 to 11 μm. The average particle diameter of the positive electrode active material is within the above range, and the migration path of lithium ions and electrons in the particles is short, so that the lithium ions and electrons in the positive electrode active material can be increasedThe transmission and diffusion performance of electrons reduces the polarization of the battery, thereby improving the cycle performance and the rate performance of the lithium ion secondary battery; in addition, the positive active material can have higher compaction density, and the energy density of the battery is improved.

The average particle size of the positive active material is in the range, which is beneficial to reducing the side reaction of the electrolyte on the surface of the positive active material and reducing the agglomeration among the positive active material particles, thereby improving the normal temperature and high temperature cycle performance and safety performance of the positive active material.

In the embodiment of the present invention, the specific surface area of the positive electrode active material is preferably 0.2m²/g～1.5m²A,/g, more preferably 0.3m²/g～1m²(ii) in terms of/g. The specific surface area of the anode active material is in the range, so that the anode active material is ensured to have higher active specific surface area, and the side reaction of the electrolyte on the surface of the anode active material is reduced, so that the capacity exertion and the cycle life of the anode active material are improved; in addition, the agglomeration among particles of the positive electrode active material during the preparation of slurry and the charging and discharging processes can be inhibited, so that the energy density and the cycle performance of the battery can be improved.

In the embodiment of the present invention, the tap density of the positive electrode active material is preferably 2.3g/cm³～2.8g/cm³. The tap density of the positive electrode active material is within the above range, which is advantageous for the lithium ion secondary battery to have high capacity performance and energy density.

In the embodiment of the present invention, the compacted density of the positive electrode active material at a pressure of 5 tons is preferably 3.1g/cm³～3.8g/cm³. The positive active material has high compaction density, and is favorable for enabling the lithium ion secondary battery to have high capacity performance and energy density.

Optionally, the morphology of the positive electrode active material particles provided by the embodiment of the invention is one or more of spherical and spheroidal.

Herein, the average particle diameter D of the positive electrode active material particles_v50 is a term well known in the art, also known as median particle diameter, and represents the volume distribution of particles of the positive electrode active material50% corresponding to the particle size. Average particle diameter D of positive electrode active material particles_v50 may be measured using apparatus and methods known in the art, for example conveniently using a laser particle size analyser, such as the Mastersizer 3000 laser particle size analyser from malvern instruments ltd, uk.

The specific surface area of the positive electrode active material is a known meaning in the art and can be measured by an apparatus and a method known in the art, for example, by a nitrogen adsorption specific surface area analysis test by a NOVA 2000e model specific surface area and pore size analyzer of corna, usa and can be calculated by a bet (brunauer Emmett teller) method. As a specific example, the test method is as follows: and taking 8.000-15.000G of the anode active material by using a weighed empty sample tube, uniformly stirring and weighing the anode active material, placing the sample tube into an NOVA 2000e degassing station for degassing, weighing the total mass of the degassed anode active material and the sample tube, and subtracting the mass of the empty sample tube from the total mass to calculate the mass G of the degassed anode active material. And (3) putting the sample tube into NOVA 2000e, measuring the adsorption quantity of nitrogen on the surface of the positive active material under different relative pressures, calculating the adsorption quantity of a monomolecular layer based on the Bronuore-Eltt-Taylor multilayer adsorption theory and the formula thereof, further calculating the total surface area A of the positive active material, and calculating the specific surface area of the positive active material through A/G.

The tap density of the positive electrode active material can be conveniently determined using instruments and methods known in the art, for example, using a tap density meter, such as a FZS4-4B tap density meter.

The compacted density of the positive electrode active material can be conveniently determined using instruments and methods known in the art, for example, using an electronic pressure tester, such as an electronic pressure tester model UTM 7305.

A method for preparing a positive electrode active material is schematically illustrated next. Any one of the above positive electrode active materials can be prepared according to the preparation method. The preparation method comprises the following steps:

and mixing the precursor of the positive active material, a lithium source and the precursor of the doping element, and sintering to obtain the positive active material.

The positive electrode active material precursor may be one or more of an oxide, a hydroxide, and a carbonate containing Ni and optionally Co and/or Mn in a stoichiometric ratio, for example, a hydroxide containing Ni, Co, and Mn in a stoichiometric ratio.

The positive electrode active material precursor may be obtained by a method known in the art, for example, by a coprecipitation method, a gel method, or a solid phase method.

As an example, a Ni source, a Co source, and a Mn source are dispersed in a solvent to obtain a mixed solution; simultaneously pumping the mixed solution, the strong base solution and the complexing agent solution into a reaction kettle with stirring by adopting a continuous parallel flow reaction mode, controlling the pH value of the reaction solution to be 10-13, controlling the temperature in the reaction kettle to be 25-90 ℃, and introducing inert gas for protection in the reaction process; after the reaction is finished, the hydroxide containing Ni, Co and Mn is obtained after aging, filtering, washing and vacuum drying.

The Ni source can be soluble nickel salt, such as one or more of nickel sulfate, nickel nitrate, nickel chloride, nickel oxalate and nickel acetate, further such as one or more of nickel sulfate and nickel nitrate, further such as nickel sulfate; the Co source can be soluble cobalt salt, such as one or more of cobalt sulfate, cobalt nitrate, cobalt chloride, cobalt oxalate and cobalt acetate, further such as one or more of cobalt sulfate and cobalt nitrate, further such as cobalt sulfate; the Mn source may be a soluble manganese salt, such as one or more of manganese sulfate, manganese nitrate, manganese chloride, manganese oxalate and manganese acetate, further such as one or more of manganese sulfate and manganese nitrate, further such as manganese sulfate.

The strong base may be one or more of LiOH, NaOH, and KOH, for example NaOH. The complexing agent can be one or more of ammonia water, ammonium sulfate, ammonium nitrate, ammonium chloride, ammonium citrate and disodium Ethylene Diamine Tetraacetate (EDTA), such as ammonia water.

The solvent of the mixed solution, the strong alkali solution and the complexing agent solution is not particularly limited, for example, the solvent of the mixed solution, the strong alkali solution and the complexing agent solution is one or more of deionized water, methanol, ethanol, acetone, isopropanol and n-hexanol, such as deionized water.

The inert gas introduced during the reaction is, for example, one or more of nitrogen, argon and helium.

The lithium source may be lithium oxide (Li)₂O), lithium phosphate (Li)₃PO₄) Lithium dihydrogen phosphate (LiH)₂PO₄) Lithium acetate (CH)₃COOLi), lithium hydroxide (LiOH), lithium carbonate (Li)₂CO₃) And lithium nitrate (LiNO)₃) One or more of (a). Further, the lithium source is one or more of lithium carbonate, lithium hydroxide and lithium nitrate; further, the lithium source is lithium carbonate.

The doping element precursor may be one or more of an oxide, a nitric acid compound, a carbonic acid compound, a hydroxyl compound and an acetic acid compound of the doping element. For example, as an oxide of a doping element, for example, titanium oxide (e.g., TiO)₂TiO, etc.), vanadium oxide (e.g. V)₂O₅、V₂O₄、V₂O₃Etc.), selenium oxide (e.g., SeO)₂Etc.), zirconia (e.g., ZrO)₂Etc.), niobium oxide (e.g., Nb)₂O₅、NbO₂Etc.), ruthenium oxide (e.g., RuO)₂Etc.), palladium oxide (e.g., PdO, etc.), antimony oxide (e.g., Sb)₂O₅、Sb₂O₃Etc.), tellurium oxide (e.g., TeO)₂Etc.) and tungsten oxide (e.g., WO)₂、WO₃Etc.).

The doping element precursor can contain a doping element with a low valence state, so that the obtained positive electrode active material has more than two different valence states in a 78% delithiation state. By "lower valence" is meant herein that the valence of the dopant element is below its highest stable valence.

The positive electrode active material precursor, the lithium source, and the doping element precursor may be mixed using a ball mill mixer or a high-speed mixer. And adding the mixed materials into an atmosphere sintering furnace for sintering. The sintering atmosphere is an oxygen-containing atmosphere, such as an air atmosphere or an oxygen atmosphere, and preferably, the oxygen concentration of the oxygen-containing atmosphere is 80% to 100%. The sintering temperature is, for example, 600 ℃ to 1000 ℃. Preferably, the sintering temperature is 600 ℃ to 900 ℃, further 700 ℃ to 900 ℃, which is beneficial to the higher distribution uniformity of the doping elements. The sintering time can be adjusted according to actual conditions, and is for example 5h to 25h, and further for example 10h to 20 h.

It should be noted that, during the preparation of the cathode active material, there are various theoretically feasible ways to regulate and control the structure and characteristics of the cathode active material, adjust the regularity of the layered structure and the position and uniformity of the doping element, and change the surface oxygen activity and average valence state of the cathode active material during the circulation process, for example, by regulating and controlling the doping element type, the doping element content, the morphology of the precursor particles of the cathode active material, the sintering time, the sintering temperature, the sintering times, the oxygen concentration during sintering, and the like during the preparation of the cathode active material. In the application, some measures of solid-phase sintering doping mode are listed, and the average valence state V of surface oxygen of the positive active material in 78% delithiation state is obtained by adjusting sintering times, doping elements in batches, controlling the overall sintering time and sintering temperature and the like_OV is-2.0 or less_OLess than or equal to-1.5. It should be understood that the methods described herein are illustrative only and are not limiting.

As an example, the doping of the doping element may be performed by dividing the doping element precursor into L batches, where L may be 1 to 5, such as 2 to 3. In these embodiments, the method of preparing the positive active material may include the steps of: mixing a positive electrode active material precursor, a lithium source and a 1 st batch of doping element precursors, and performing 1 st sintering treatment; then mixing the product of the 1 st sintering treatment with the 2 nd batch of doping element precursor, and carrying out the 2 nd sintering treatment; and repeating the steps until the product of the L-1 th sintering treatment is mixed with the L-th batch of doped element precursors, and performing the L-th sintering treatment to obtain the cathode active material.

The doping of L batches may be performed by equally dividing the doping element precursor into L portions or arbitrarily dividing the doping element precursor into L portions.

The temperature of each sintering process may be the same or different. The time for each sintering process may be the same or different. The sintering temperature and time can be adjusted by those skilled in the art according to the kind and amount of the doping element. For example, the temperature of each sintering process may be 600 ℃ to 1000 ℃, such as 600 ℃ to 900 ℃, and further such as 700 ℃ to 900 ℃; the time of each sintering treatment can be 1-20 h, such as 2-18 h; the total sintering time may be 5h to 25h, such as 10h to 20 h.

In the doping process, the doping uniformity may be improved, for example, by increasing the sintering temperature and/or the sintering time within a certain range.

In some embodiments, the sintered product may also be subjected to a crushing process and a sieving process to obtain a cathode active material having an optimized particle size distribution and specific surface area. The crushing mode is not particularly limited, and may be selected according to actual requirements, for example, a particle crusher is used.

Positive pole piece

The second aspect of the embodiments of the present invention provides a positive electrode plate, where the positive electrode plate adopts the positive electrode active material according to the first aspect of the embodiments of the present invention.

Due to the adoption of the positive active material, the positive pole piece disclosed by the embodiment of the invention can enable the lithium-ion secondary battery to simultaneously have good normal-temperature and high-temperature cycle performance and higher energy density.

Specifically, the positive electrode plate comprises a positive electrode current collector and a positive electrode active material layer arranged on at least one surface of the positive electrode current collector. For example, the positive electrode current collector includes two opposite surfaces in a thickness direction thereof, and the positive electrode active material layer is stacked on either or both of the two surfaces of the positive electrode current collector.

The positive electrode active material layer includes the positive electrode active material of the first aspect of the embodiment of the invention.

In addition, the positive electrode active material layer may further include a conductive agent and a binder. The types of the conductive agent and the binder in the positive electrode active material layer are not particularly limited, and can be selected according to actual requirements.

As an example, the conductive agent may be one or more of graphite, superconducting carbon, acetylene black, carbon black, ketjen black, carbon dots, carbon nanotubes, graphene, and carbon nanofibers; the binder may be one or more of Styrene Butadiene Rubber (SBR), water-based acrylic resin (water-based acrylic resin), carboxymethyl cellulose (CMC), polyvinylidene fluoride (PVDF), Polytetrafluoroethylene (PTFE), polyvinyl butyral (PVB), ethylene-vinyl acetate copolymer (EVA), vinylidene fluoride-tetrafluoroethylene-propylene terpolymer, vinylidene fluoride-hexafluoropropylene-tetrafluoroethylene terpolymer, tetrafluoroethylene-hexafluoropropylene copolymer, fluorine-containing acrylic resin, and polyvinyl alcohol (PVA).

The positive current collector can be made of metal foil or porous metal plate with good conductivity and mechanical property, and the material of the positive current collector can be one or more of aluminum, copper, nickel, titanium, silver and their respective alloys. The positive electrode collector is, for example, an aluminum foil.

The positive pole piece can be prepared according to the conventional method in the field. For example, the positive electrode active material, the conductive agent and the binder are dispersed in a solvent, wherein the solvent can be N-methyl pyrrolidone (NMP) or deionized water, so as to form uniform positive electrode slurry, the positive electrode slurry is coated on a positive electrode current collector, and the positive electrode pole piece is obtained after the procedures of drying, rolling and the like.

Lithium ion secondary battery

The third aspect of the embodiments of the present invention provides a lithium ion secondary battery, where the lithium ion battery includes a positive electrode plate, a negative electrode plate, a separator, and an electrolyte, where the positive electrode plate is the positive electrode plate of the second aspect of the embodiments of the present invention.

By adopting the positive active material of the first aspect of the embodiment of the invention, the lithium ion secondary battery can simultaneously give consideration to good normal-temperature and high-temperature cycle performance and higher energy density.

The negative electrode plate can be a metal lithium plate.

The negative electrode plate can also comprise a negative electrode current collector and a negative electrode active material layer arranged on at least one surface of the negative electrode current collector. For example, the negative electrode current collector includes two opposite surfaces in a thickness direction thereof, and the negative electrode active material layer is stacked on either or both of the two surfaces of the negative electrode current collector.

The anode active material layer includes an anode active material. The kind of the negative electrode active material in the embodiment of the present invention is not particularly limited, and may be selected according to actual needs. As an example, the negative active material may be natural graphite, artificial graphite, mesophase micro carbon spheres (MCMB), hard carbon, soft carbon, silicon-carbon composite, SiO_m(0<m<2, e.g. m ═ 1), Li-Sn alloys, Li-Sn-O alloys, Sn, SnO₂Lithium titanate Li of spinel structure₄Ti₅O₁₂One or more of Li-Al alloy and metallic lithium.

The anode active material layer may further include a conductive agent and a binder. The embodiment of the present invention does not specifically limit the types of the conductive agent and the binder in the negative electrode active material layer, and may be selected according to actual needs. As an example, the conductive agent is one or more of graphite, superconducting carbon, acetylene black, carbon black, ketjen black, carbon dots, carbon nanotubes, graphene, and carbon nanofibers; the binder is one or more of Styrene Butadiene Rubber (SBR), polyvinylidene fluoride (PVDF), Polytetrafluoroethylene (PTFE), polyvinyl butyral (PVB), water-based acrylic resin (water-based acrylic resin) and carboxymethyl cellulose (CMC).

The negative electrode active material layer may further optionally include a thickener such as carboxymethyl cellulose (CMC).

The negative current collector can be made of metal foil or porous metal plate with good conductivity and mechanical property, and the material of the negative current collector can be one or more of copper, nickel, titanium, iron and their respective alloys. The negative electrode collector is, for example, a copper foil.

The negative pole piece can be prepared according to the conventional method in the field. For example, a negative electrode active material, a conductive agent, a binder and a thickening agent are dispersed in a solvent, wherein the solvent can be N-methyl pyrrolidone (NMP) or deionized water, so as to form uniform negative electrode slurry, the negative electrode slurry is coated on a negative electrode current collector, and the negative electrode pole piece is obtained after the working procedures of drying, rolling and the like.

In the lithium ion secondary battery according to the embodiment of the present invention, the electrolyte may be a solid electrolyte, such as a polymer electrolyte, an inorganic solid electrolyte, or the like, but is not limited thereto. The electrolyte may be an electrolytic solution. The electrolyte solution includes a solvent and a lithium salt dissolved in the solvent.

The solvent may be a non-aqueous organic solvent, for example, one or more, preferably two or more, of Ethylene Carbonate (EC), Propylene Carbonate (PC), Ethyl Methyl Carbonate (EMC), diethyl carbonate (DEC), dimethyl carbonate (DMC), dipropyl carbonate (DPC), Methyl Propyl Carbonate (MPC), Ethyl Propyl Carbonate (EPC), Methyl Formate (MF), Methyl Acetate (MA), Ethyl Acetate (EA), Propyl Acetate (PA), Methyl Propionate (MP), Ethyl Propionate (EP), Propyl Propionate (PP), Methyl Butyrate (MB), and Ethyl Butyrate (EB).

The lithium salt may be LiPF₆(lithium hexafluorophosphate), LiBF₄Lithium tetrafluoroborate (LiClO), LiClO₄(lithium perchlorate) LiAsF₆(lithium hexafluoroarsenate), LiFSI (lithium bis (fluorosulfonylimide)), LiTFSI (lithium bis (trifluoromethanesulfonylimide)), LiTFS (lithium trifluoromethanesulfonate), LiDFOB (lithium difluorooxalato borate), LiBOB (lithium bis (oxalato borate)), LiPO₂F₂One or more of (lithium difluorophosphate), LiDFOP (lithium difluorooxalate phosphate) and LiTFOP (lithium tetrafluorooxalate phosphate), for example LiPF₆(lithium hexafluorophosphate), LiBF₄(lithium tetrafluoroborate), LiBOB (lithium bis (oxalato) borate), LiDFOB (lithium difluoro (oxalato) borate), LiTFSI (lithium bis (trifluoromethanesulfonyl) imide), and LiFSI (lithium bis (fluorosulfonyl) imide).

The electrolyte may optionally contain other additives such as Vinylene Carbonate (VC), ethylene carbonate (VEC), fluoroethylene carbonate (FEC), difluoroethylene carbonate (DFEC), trifluoromethyl ethylene carbonate (TFPC), Succinonitrile (SN), Adiponitrile (ADN), Glutaronitrile (GLN), Hexanetricarbonitrile (HTN), 1, 3-propanesultone (1,3-PS), vinyl sulfate (DTD), Methylene Methanedisulfonate (MMDS), 1-propene-1, 3-sultone (PST), 4-methyl-ethylene sulfate (PCS), 4-ethyl-ethylene sulfate (PES), 4-propyl-ethylene sulfate (PEGLST), propylene sulfate (TS), 1, 4-butane sultone (1,4-BS), ethylene sulfite (DTO), dimethyl sulfite (DMS), One or more of Diethylsulfite (DES), cyclic quaternary ammonium sulfonate, tris (trimethylsilane) phosphate (TMSP), and tris (trimethylsilane) borate (TMSB), but is not limited thereto.

The lithium ion secondary battery according to the embodiment of the present invention is not particularly limited to the separator, and any known separator having a porous structure with electrochemical stability and mechanical stability, such as a single-layer or multi-layer film of one or more of glass fiber, non-woven fabric, Polyethylene (PE), polypropylene (PP), and polyvinylidene fluoride (PVDF), may be used.

The positive pole pieces and the negative pole pieces are alternately stacked, and the isolating film is arranged between the positive pole pieces and the negative pole pieces to play an isolating role, so that the battery cell is obtained, or the battery cell can be obtained after winding. And placing the battery cell in a shell, injecting electrolyte, and sealing to obtain the lithium ion secondary battery.

Examples

The present disclosure is more particularly described in the following examples that are intended as illustrations only, since various modifications and changes within the scope of the present disclosure will be apparent to those skilled in the art. Unless otherwise indicated, all parts, percentages, and ratios reported in the following examples are on a weight basis, and all reagents used in the examples are commercially available or synthesized according to conventional methods and can be used directly without further treatment, and the equipment used in the examples is commercially available.

Example 1

Preparation of positive electrode active material

Doping element Sb, and oxidizing antimony Sb as precursor of the doping element₂O₃The doping of Sb was performed approximately equally divided into 2 batches. The preparation method comprises the following steps:

preparing a precursor [ Ni ] of the positive electrode active material_0.8Co_0.1Mn_0.1](OH)₂Adding lithium hydroxide LiOH and antimony oxide of the 1 st batch into a high-speed mixer to mix for 1h to obtain a mixed material, wherein the molar ratio Li/Me of the precursor of the positive active material to the lithium hydroxide is 1.05, and Me represents the total molar amount of Ni, Co and Mn in the precursor of the positive active material; putting the mixed material into an atmosphere sintering furnace for sintering for the 1 st time, wherein the sintering temperature is 850 ℃, the sintering time is 8h, and the sintering atmosphere is O₂An oxygen-containing atmosphere having a concentration of 90%.

And adding the product of the 1 st sintering treatment and the 2 nd batch of antimony oxide into a high-speed mixer for mixing for 1h, and performing 2 nd sintering, wherein the sintering temperature and the sintering atmosphere are the same as those of the 1 st sintering, and the sintering time is 12h, namely the total sintering time is 20 h.

And crushing and sieving the product obtained after the 2 nd sintering treatment to obtain the high-nickel ternary positive electrode active material. The amount of antimony oxide added was such that the true doping concentration of Sb in the positive electrode active material was 25090. mu.g/cm³. As shown in fig. 1, Sb is uniformly distributed in the positive electrode active material particles.

Preparation of the electrolyte

Mixing EC, DEC and DMC according to the volume ratio of 1:1:1 to obtain a solvent, and then adding lithium salt LiPF₆Dissolving in the above solvent to obtain an electrolyte solution, wherein LiPF₆The concentration of (2) is 1 mol/L.

Preparation of button cell

Dispersing the prepared positive electrode active material, conductive carbon black and binder PVDF into solvent N-methylpyrrolidone (NMP) according to the weight ratio of 90:5:5, and uniformly mixing to obtain positive electrode slurry; and uniformly coating the positive electrode slurry on a positive current collector aluminum foil, and drying and cold pressing to obtain the positive electrode piece.

And in the button cell, sequentially stacking the positive pole piece, the isolating membrane and the metal lithium piece, injecting the electrolyte, and assembling to obtain the button cell.

Preparation of full cell

Dispersing the prepared positive electrode active material, conductive agent acetylene black and binder PVDF into solvent NMP according to the weight ratio of 94:3:3, and uniformly mixing to obtain positive electrode slurry; and uniformly coating the positive electrode slurry on a positive current collector aluminum foil, and drying and cold pressing to obtain the positive electrode piece.

Dispersing a negative electrode active material artificial graphite, hard carbon, a conductive agent acetylene black, a binder Styrene Butadiene Rubber (SBR) and a thickening agent sodium carboxymethyl cellulose (CMC) into deionized water according to a weight ratio of 90:5:2:2:1, and uniformly mixing to obtain negative electrode slurry; and uniformly coating the negative electrode slurry on a negative current collector aluminum foil, and drying and cold pressing to obtain a negative electrode plate.

Polyethylene (PE) porous polymeric films were used as separators. And stacking the positive pole piece, the isolating membrane and the negative pole piece in sequence to obtain a naked electric core, placing the naked electric core in an external package, injecting the electrolyte and packaging to obtain the full battery.

Examples 2 to 13, examples 16 to 21 and comparative examples 1 to 2

Different from the embodiment 1, the relevant parameters in the preparation step of the positive active material are changed, and the types, the content of each batch and the sintering temperature when doping elements are mixed are adjusted to be 650-850 ℃, and the total sintering time is adjusted to be 10-20 h, so that the positive active material with the preset doping element types, doping amount and doping uniformity is obtained; examples 4 and 12, in which multi-element doping is involved, each doping element content is substantially the same; no doping element was added in comparative example 1; the remaining parameters are shown in Table 1.

Examples 14 and 15

Different from the embodiment 1, the doping element is added in a single batch in the embodiment 14, and the sintering temperature is 715 ℃; the doping elements in the embodiment 15 are added in a single batch, and the sintering temperature is 670 ℃; the remaining parameters are shown in Table 1.

Examples 22 and 23

Different from the embodiment 1, the temperature of the 1 st sintering in the embodiment 22 is 810 ℃ and the time is 12h, the temperature of the 2 nd sintering is 660 ℃ and the time is 2h, wherein the 2 nd batch doping element accounts for 65 percent of the total doping element content;

unlike example 1, in example 23, the temperature of the 1 st sintering was 790 ℃ and the time was 7 hours, and the temperature of the 2 nd sintering was 630 ℃ and the time was 2 hours, wherein the 2 nd doping element accounted for 75% of the total doping element content.

Examples 24 and 25 and comparative examples 3 and 4

Unlike example 1, the precursors of the positive electrode active materials of examples 24 and 25 and comparative example 4 were [ Ni ]_0.5Co_0.2Mn_0.3](OH)₂The types of the mixed doping elements are different; the precursor of the positive electrode active material of comparative example 3 was [ Ni ]_0.5Co_0.2Mn_0.3](OH)₂No doping element is added; the remaining parameters are shown in Table 1.

Test section

1) Surface oxygen average valence V of 78% delithiation state positive electrode active material_OAnd testing the valence of the doping element M

At 25 ℃, 18 button cells are respectively charged to the upper limit of the charge-discharge cut-off voltage by a constant current of 1C, then are charged to the current of less than or equal to 0.05mA by a constant voltage, and are placed for 2 minutes, and then are discharged to the lower limit of the charge-discharge cut-off voltage by the constant current of 1C.

Then, the 18 button cells after the charge and discharge were charged to 2.8V, 2.9V, 3.0V, 3.1V, 3.2V, 3.3V, …, 4.0V, 4.1V, 4.2V, 4.3V, 4.4V, and 4.5V, respectively, at a rate of 0.1C (i.e., the charging voltage interval was 0.1V). Taking each charged button cell, disassembling a positive pole piece in a drying room to be used as a sample, weighing and recording the mass of the sample, putting the sample into a digestion tank, slowly adding 10mL of aqua regia to be used as a digestion reagent, then putting the digestion reagent into a CEM-Mars5 microwave digestion instrument, and digesting the sample at 2450Hz microwave emission frequency; transferring the digested sample solution into a volumetric flask, shaking up, sampling, putting into a 7000DV type ICP-OES sample introduction system of the American Platinum Elmer (PE), testing the mass concentration of Li, O, Ni, Co, Mn and doping elements on the positive active material at the argon pressure of 0.6MPa and the radio frequency power of 1300W, converting based on the mass concentration of each element to obtain a chemical formula under each voltage, and further obtaining the lithium removal state under each voltage. The chemical formula of the positive electrode active material is Li when converted by ICP-OES test_0.22Ni_0.8Co_0.1Mn_0.1O₂If the voltage is equal to 78%, the corresponding delithiated state is (1-0.22) × 100%, and the corresponding voltage is the voltage corresponding to 78% delithiated state.

Charging a battery containing a positive active material to be detected to a voltage corresponding to a 78% delithiation state, then disassembling the battery in a drying room by using scissors, taking out the whole positive pole piece, putting the positive pole piece into a beaker, pouring a proper amount of high-purity anhydrous dimethyl carbonate (DMC), continuously cleaning for 3 times by replacing the DMC every 8 hours, then putting the positive pole piece into a vacuum standing box of the drying room, keeping the vacuumizing state at-0.096 MPa, and drying for 12 hours; the dried positive electrode piece was used as an XPS test sample.

And (3) sticking the pole piece sample on a sample table of AXIS Supra XPS of Kratos through a 3M insulating adhesive tape, automatically feeding a sample, and vacuumizing for at least 1 h. Using a monochromatic Al target (Al K alpha, 1486.6eV) as an excitation source, performing full-spectrum scanning with a 1eV step size and 160eV pass energy, performing fine-spectrum scanning of oxygen elements and doping elements with a 0.1eV step size and 40eV pass energy, and using XPSpeak peak splitting software and C peak splitting software_1sThe binding energy of (a) is 284.8eV for charge correction; for photoelectron peaks of p, d and f levels, the peak intensity ratio of splitting peaks is set as follows: p is a radical of_1/2:p_3/2＝1:2，d_3/2:d_5/2＝2:3，f_5/2:f_7/2The valence state of the element is determined by peak separation versus the standard XPS characteristic peak of the target specific element, 3: 4.

2) Oxygen defect formation energy Δ E of "78% delithiated" positive electrode active material_O-vacTest (2)

(1) According to JIS K0131-1996X-ray diffraction analysis general rule, a BRUKER D8DISCOVER type X-ray diffractometer is adopted to use CuK_αThe radiation is radiation source, and the wavelength of the radiationThe scanning 2 theta angle range is 15-70 degrees, the scanning speed is 4 degrees/min, and XRD analysis is carried out on the 78% delithiation state positive electrode active material. Based on XRD results, information such as unit cell parameters, element occupation and the like of the positive active material in the 78% delithiation state is obtained, and accordingly, a bulk structure model of the positive active material with a complete structure in the 78% delithiation state is constructedForm of a structure satisfyingUsing a computing software VASP based on a first principle of a density functional theory to exchange a correlation functional by adopting GGA + U, performing structure optimization on the model until the energy is converged, extracting the optimized structure energy, and recording the structure energy as E_pristine。

(2) Deducting an oxygen atom on the basis of the optimized 78% delithiation-state positive active material bulk phase structure model to obtain a 78% delithiation-state bulk phase model of the positive active material with oxygen defects, exchanging a correlation functional by using a computing software VASP based on a first principle of a density functional theory, performing structure optimization on the oxygen defect-containing bulk phase model until energy convergence, extracting optimized structure energy, and marking as E_defect。

(3) Using computing software VASP based on the first principle of the density functional theory, adopting GGA + U to exchange the correlation functional, optimizing oxygen molecules until energy convergence, extracting the optimized oxygen energy divided by 2, and recording as E_O。

(4) Will E_pristine、E_defectAnd E_OThe oxygen defect formation energy of one oxygen atom is calculated by substituting the value of (2) into the formula (1) described above.

Subtracting different oxygen atoms with reference to the step (2) to obtain defect formation energies of the different oxygen atoms, and selecting the minimum value as the oxygen defect formation energy Δ E of the bulk structure of the positive electrode active material in the "78% delithiation state_O-vac。

In the steps (1), (2) and (3), the precision of each parameter is equal to or higher than the following parameters:

3) mass concentration deviation σ test of doping element at any point in secondary particle

(1) Mass concentration testing of doping elements at different sites in secondary particles

Weighing 2g of positive active material powder sample, uniformly sprinkling the sample on a sample table adhered with conductive adhesive, slightly pressing to fix the powder, or cutting out a pole piece of 1cm multiplied by 1cm from a battery positive pole piece, and adhering the pole piece to the sample table to serve as a sample to be detected. The sample stage was set in a vacuum sample chamber and fixed, a cross section of the secondary particle was prepared using an argon ion cross section polisher type IB-09010CP from Japan Electronics (JEOL) corporation, points were taken at 17 positions of the cross section of the secondary particle as shown in fig. 2, the area of each point was 20nm × 20nm, and the mass concentration of the doping element at the 17 points was measured using an X-Max type energy spectrometer (EDS) from oxford instruments group, uk, in combination with a Scanning Electron Microscope (SEM) type Sigma-02-33 from ZEISS, germany, by the following test method: selecting Li, O, Ni, Co, Mn and doping elements as detection elements, setting SEM parameters of 20kV acceleration voltage, 60 mu m light bar, working distance of 8.5mm and current of 2.335A, stopping testing when spectrogram area reaches more than 250000cts (controlled by acquisition time and acquisition rate) during EDS-SEM test, and acquiring data to obtain mass concentration eta of the doping elements at each site₁、η₂、η₃、…、η₁₇。

(2) Average mass concentration of doping element in secondary particleTest (2)

By the EDS-SEM test method, as shown by the dotted line box in FIG. 2, the test area covers all the points of the secondary particle point scan and does not exceed the cross section of the secondary particle.

(3) Calculating the mass concentration deviation sigma of the doping element at any point in the secondary particles

And (4) calculating the mass concentration deviation sigma of the doping element at any point in the secondary particles according to the formula (2).

4) True doping concentration ω test of the positive electrode active material:

the true density rho of the positive active material was measured using a TD2400 type powder true density tester from Peking Piaode electronics Co., Ltd_TrueThe test method is as follows: taking a certain mass of positive electrode at 25 DEG CPlacing the active material in a sample cup, and recording the mass m of the positive active material; putting a sample cup filled with the positive active material into a test cavity of a true density instrument, sealing a test system, introducing inert gas with small molecular diameter such as helium or nitrogen, detecting the pressure of the gas in a sample chamber and an expansion chamber, measuring the true volume V of the tested material according to the Bohr's law PV-nRT, and calculating the true density rho of the secondary particles by m/V_True. Wherein n is the molar amount of gas in the sample cup; taking 8.314 as an ideal gas constant; t is ambient temperature and 298.15K.

The mass concentration of the doping element in the positive active material was measured by using an ICP-OES model 7000DV of Platinum Elmer (PE) of AmericaThe test method is as follows: punching a pole piece containing the positive active material into a wafer with the total mass of more than 0.5g or taking at least 5g of a positive active material powder sample, weighing and recording the mass of the sample, putting the sample into a digestion tank, slowly adding 10mL of aqua regia as a digestion reagent, putting the sample into a Mars5 type microwave digestion instrument of the American CEM company after assembly, and digesting the sample at the microwave emission frequency of 2450 Hz; transferring the digested sample solution into a volumetric flask, shaking uniformly, sampling, putting into a sample injection system of PE7000DV type ICP-OES, and testing the mass concentration of the doping elements in the positive active material by using argon pressure of 0.6MPa and radio frequency power of 1300W.

The true doping concentration ω of the positive electrode active material is then calculated according to the formula (3) described earlier.

In order to test the positive active material in the whole battery, the battery can be disassembled in a drying room, the middle part of a positive pole piece is taken out and put into a beaker, a proper amount of high-purity anhydrous dimethyl carbonate DMC is poured, DMC is replaced every 8 hours, the continuous cleaning is carried out for 3 times, then the positive pole piece is put into a vacuum standing box of the drying room, the vacuumizing state is kept (-0.096MPa), the drying is carried out for 12 hours, and a pole piece sample with a preset size is cut out after the drying for testing; or a predetermined mass of the positive active material powder was scraped in a dry room with a blade as a test sample.

5) Calculation of the cathode active Material according to the formula (4) described previouslyMass concentration of medium doping elementWith the average mass concentration of the doping element in the secondary particlesOf (c) is calculated.

6) Initial gram capacity test for button cell

And charging the battery to the upper limit of a charge-discharge cut-off voltage at a constant current of 0.1 ℃ at 25 ℃, then charging the battery to a constant voltage until the current is less than or equal to 0.05mA, standing for 2 minutes, and then discharging the battery to the lower limit of the charge-discharge cut-off voltage at a constant current of 0.1 ℃, wherein the discharge capacity at this time is the initial gram capacity of the button battery.

7) Initial gram capacity test of full cell

Charging the battery to the upper limit of a charge-discharge cut-off voltage at a constant current of 1/3 ℃ at 25 ℃, then charging the battery to a constant voltage until the current is less than or equal to 0.05mA, standing the battery for 5 minutes, and then discharging the battery to the lower limit of the charge-discharge cut-off voltage at a constant current of 1/3 ℃, wherein the discharge capacity at this time is the initial gram capacity of the whole battery.

8) High temperature cycle performance testing of full cells

Charging the battery at a constant current of 1C to the upper limit of the cut-off voltage of charge and discharge at 45 ℃, then charging the battery at a constant voltage until the current is less than or equal to 0.05mA, standing the battery for 5 minutes, and then discharging the battery at a constant current of 1C to the lower limit of the cut-off voltage of charge and discharge, which is a charge and discharge cycle, wherein the discharge capacity of the cycle is recorded as the discharge specific capacity D of the 1 st cycle₁. The battery is subjected to 400 times of cyclic charge and discharge tests according to the method, and the specific discharge capacity D of the 400 th cycle is recorded₄₀₀。

Capacity retention (%) of the full cell at 45 ℃ and 400 cycles of 1C/1C₄₀₀/D₁×100％

In the above test: in examples 1 to 23 and comparative examples 1 to 2, the charge-discharge cut-off voltage of the button cell battery is 2.8V to 4.25V, and the charge-discharge cut-off voltage of the full cell battery is 2.8V to 4.2V; in examples 24 to 25 and comparative examples 3 to 4, the charge-discharge cut-off voltage of the button cell battery was 2.8V to 4.35V, and the charge-discharge cut-off voltage of the full cell was 2.8V to 4.3V.

The test results of examples 1 to 25 and comparative examples 1 to 4 are shown in tables 1 and 2.

TABLE 1

In table 1, the valency is the lowest valence and the highest valence showing the doping element; the mass ratio of each batch of the precursor to the precursor of the doping element of the 1 st batch to the precursor of the doping element of the 2 nd batch is equal to the mass ratio of the precursor of the doping element of the 1 st batch to the mass of the precursor of the doping element of the 2 nd batch.

TABLE 2

As can be seen from the results of comparing examples 1 to 21 with comparative examples 1 to 2, and examples 24 to 25 with comparative examples 3 to 4, by including the doping element M in the transition metal site of the positive electrode active material, the valence of the doping element M is +3 or more, and the surface oxygen average valence V of the positive electrode active material in 78% delithiated state_OIs-2.0 to-1.5, and the lithium ion secondary battery not only has higher initial gram capacity, but also has higher high-temperature cycle performance.

From the results of examples 1 and 5 to 12, it can be seen that when the doping amount is too small, the stability of the doping element to the structure of the positive electrode material is not sufficiently improved, so that the capacity of the battery is low, and the high-temperature cycle performance is poor. When the doping amount exceeds 49100 mu g/cm³When the doping concentration is too high, the original anode structure is damaged, and the capacity and 45 ℃ cycle performance of the battery are not as good as those of the battery with the true doping concentration of 2300 mug/cm³～49100μg/cm³The positive electrode active material of (1).

From the results of examples 13 to 15, it can be seen that when the mass concentration deviation of the doping element at any point in the secondary particles is less than 20%, the doping element is very uniformly distributed in the active material, the stability of the material is obviously improved, and the capacity and the cycle performance of the corresponding battery cell are excellent; on the contrary, when the deviation of the doping elements at different positions exceeds 20%, the lattice stress of the doping non-uniform region is large, and the capacity and the high-temperature cycle performance of the battery are deteriorated.

As can be seen from the results of examples 1, 22, and 23, when the deviation ∈ between the mass concentration of the doping element in the positive electrode active material and the average mass concentration of the doping element in the secondary particles was 30% or less, it was demonstrated that a large amount of the doping element could be doped into the secondary particles, the effect of the doping element on improving the structural stability of the positive electrode material was sufficiently exerted, and the battery capacity and the high-temperature cycle performance were improved. When epsilon is more than 30%, more doping elements are distributed in gaps or surfaces of the secondary particles, the improvement effect of the doping elements on the positive active material is poor, but the doping elements distributed on the surfaces play a certain role in coating and isolating side reaction of the electrolyte, so that the capacity and the high-temperature cycle performance of the battery cell are slightly reduced.

While the invention has been described with reference to specific embodiments, the invention is not limited thereto, and various equivalent modifications and substitutions can be easily made by those skilled in the art within the technical scope of the invention. Therefore, the protection scope of the present invention shall be subject to the protection scope of the claims.