# Patent

## Title
Cathode active material and method of preparing the same

## Abstract

Provided are a cathode active material including polycrystalline lithium manganese oxide and a boron-containing coating layer on a surface of the polycrystalline lithium manganese oxide, and a method preparing the same. Since the cathode active material according to an embodiment of the present invention may prevent direct contact between the polycrystalline lithium manganese oxide and an electrolyte solution by including the boron-containing coating layer on the surface of the polycrystalline lithium manganese oxide, the cathode active material may prevent side reactions between the cathode active material and the electrolyte solution. In addition, since limitations, such as the Jahn-Teller distortion and the dissolution of Mn2+, may be addressed by structurally stabilizing the polycrystalline lithium manganese oxide, tap density, life characteristics, and charge and discharge capacity characteristics of a secondary battery may be improved.

## Background
CROSS-REFERENCE TO RELATED APPLICATIONS
The present application is a continuation of International Application No. PCT/KR2014/006843 filed Jul. 25, 2014, which claims priority from Korean Application No. 10-2013-0089071 filed Jul. 26, 2013, the disclosures of which are hereby incorporated herein by reference.


TECHNICAL FIELD
The present invention relates to a cathode active material and a method of preparing the same, and more particularly, to a cathode active material having a boron-containing coating layer on the surface of polycrystalline lithium manganese oxide particles, and a method of preparing the same.
BACKGROUND ART
In line with growing concerns about environmental issues, research into electric vehicles and hybrid electric vehicles which may replace vehicles using fossil fuels such as gasoline vehicles and diesel vehicles, one of major causes of air pollution, has been conducted.
Research into the use of lithium secondary batteries having high energy density as power sources of the electric vehicles and hybrid electric vehicles has been actively conducted, and some of the research are in a commercialization stage.
Lithium cobalt oxide (LiCoO2) is mainly used as a cathode active material of the lithium secondary batteries, and in addition, the uses of lithium manganese oxides, such as LiMnO2 having a layered crystal structure and LiMn2O4 having a spinel crystal structure, and lithium nickel oxide (LiNiO2) are also in consideration.
Among these materials, lithium manganese oxides, such as LiMn2O4, have advantages in that thermal stabilities are excellent and the prices are relatively low, but may have limitations in that capacities are low, cycle characteristics are poor, and high-temperature characteristics are poor.
When considering the structure of LiMn2O4, lithium (Li) ions are located at tetrahedral sites (8a), manganese (Mn) ions (Mn3+/Mn4+) are located at octahedral sites (16d), and O2− ions are located at octahedral sites (16c). These ions form a cubic close-packed arrangement. The 8a tetrahedral sites share faces with the 16c octahedral sites having vacancies therearound to form three-dimensional channels, thereby providing the channels through which Li+ ions are easily move.
In particular, the biggest limitation of LiMn2O4 is that the capacity decreases as the number of cycles increases. This is due to a structural change known as the “Jahn-Teller distortion”, that is, a phase transition from cubic to tetragonal caused by changes in the oxidation number of Mn ion at the end of discharge (near 3 V). Also, the cause of the capacity fading may include a phenomenon of dissolution of manganese into an electrolyte solution.
In order to address these limitations, a significant amount of research into a method of excessively adding Li in an amount of 1.01 to 1.1 times the stoichiometric amount of Li to stoichiometric LiMn2O4 to prevent the site exchange between Li and Mn metal ions and a method of substituting Mn sites with transition metals or divalent and trivalent cations to control the oxidation number of Mn ion or prevent the phase transition from cubic to tetragonal has been conducted.
These methods may reduce the capacity fading in comparison to that of the stoichiometric LiMn2O4, but may not address the limitations such as the Jahn-Teller distortion and the dissolution of Mn2+.
PRIOR ART DOCUMENTS
Patent Document
Korean Patent Application Laid-Open Publication No. 1999-018077
DISCLOSURE OF THE INVENTION
Technical Problem
An aspect of the present invention provides a cathode active material which may prevent side reactions between the cathode active material and an electrolyte solution, and may improve tap density, life characteristics, and charge and discharge capacity characteristics of a secondary battery by addressing limitations such as the Jahn-Teller distortion and the dissolution of Mn2+.
Another aspect of the present invention provides a method of preparing the cathode active material.
Another aspect of the present invention provides a cathode including the cathode active material.
Another aspect of the present invention provides a lithium secondary battery including the cathode.
Technical Solution
According to an aspect of the present invention, there is provided a cathode active material including: polycrystalline lithium manganese oxide; and a boron-containing coating layer on a surface of the polycrystalline lithium manganese oxide.
According to another aspect of the present invention, there is provided a method of preparing the cathode active material including: (i) coating a surface of a polycrystalline manganese precursor with a boron-containing compound by mixing the polycrystalline manganese precursor and a boron precursor and performing a heat treatment; and (ii) forming a boron-containing coating layer on a surface of polycrystalline lithium manganese oxide by mixing the manganese precursor coated with the boron-containing compound and a lithium precursor and sintering the mixture.
According to another aspect of the present invention, there is provided a method of preparing the cathode active material including mixing a polycrystalline manganese precursor, a boron precursor, and a lithium precursor, and sintering the mixture.
According to another aspect of the present invention, there is provided a cathode including the cathode active material.
According to another aspect of the present invention, there is provided a lithium secondary battery including the cathode.
Advantageous Effects
Since a cathode active material according to an embodiment of the present invention may prevent direct contact between polycrystalline lithium manganese oxide and electrolyte solution by including a boron-containing coating layer on the surface of the polycrystalline lithium manganese oxide, the cathode active material may prevent side reactions between the cathode active material and the electrolyte solution. In addition, since limitations, such as the Jahn-Teller distortion and the dissolution of Mn2+, may be addressed by structurally stabilizing the lithium manganese oxide, tap density, life characteristics, and charge and discharge capacity characteristics of a secondary battery may be improved.
Also, according to a preparation method according to an embodiment of the present invention, crystals of polycrystalline lithium manganese oxide may be easily grown at low temperature and the surface of the polycrystalline lithium manganese oxide may be uniformly coated with a boron-containing coating layer.



BRIEF DESCRIPTION OF THE DRAWINGS
The following drawings attached to the specification illustrate preferred examples of the present invention by example, and serve to enable technical concepts of the present invention to be further understood together with detailed description of the invention given below, and therefore the present invention should not be interpreted only with matters in such drawings.
FIG. 1 is a schematic view illustrating a cathode active material according to an embodiment of the present invention;
FIG. 2 illustrates a scanning electron microscope (SEM) image of a cathode active material prepared in Example 1 of the present invention;
FIG. 3 illustrates an SEM image of a cathode active material prepared in Example 2 of the present invention;
FIG. 4 illustrates an SEM image of a cathode active material prepared in Comparative Example 1 of the present invention; and
FIG. 5 illustrates an SEM image of a cathode active material prepared in Comparative Example 2 of the present invention.



MODE FOR CARRYING OUT THE INVENTION
Hereinafter, the present invention will be described in more detail to allow for a clearer understanding of the present invention.
It will be understood that words or terms used in the specification and claims shall not be interpreted as the meaning defined in commonly used dictionaries. It will be further understood that the words or terms should be interpreted as having a meaning that is consistent with their meaning in the context of the relevant art and the technical idea of the invention, based on the principle that an inventor may properly define the meaning of the words or terms to best explain the invention.
As illustrated in FIG. 1, a cathode active material according to an embodiment of the present invention may include polycrystalline lithium manganese oxide; and a boron-containing coating layer on the surface of the polycrystalline lithium manganese oxide.
In general, spinel-structured lithium manganese oxide, e.g., LiMn2O4, has limitations such as the possibility of the fast diffusion of lithium ions due to its structural characteristics of having a lithium movement path, high capacity but the instability of an electrolyte in a high voltage range, the Jahn-Teller distortion of Mn3+ during heavy discharge, and the dissolution of manganese ions (Mn2+) during discharge.
Specifically, in LiMn2O4, Mn3+ relatively increases in comparison to Mn4+ under the condition in which lithium ions are insufficient in the lattice or under heavy discharge conditions. As a result, the distortion of the structure occurs, and a phase transition from cubic to tetragonal occurs due to the changes in the oxidation number of Mn ions during continuous charge and discharge caused by the increase in unstable Mn3+. Eventually, the reversibility of the structure may be reduced.
Also, the dissolution of Mn ions eventually causes capacity fading while unstable Mn3+ changes to Mn2+ and Mn4+ on the surface of an electrode through an exchange reaction between the Mn3+ ions, the generated Mn2+ ions are dissolved in an acidic electrolyte to decrease the amount of an active material, and the dissolved Mn2+ ions are precipitated as metal at an anode to obstruct the movement of lithium ions. Thus, the dissolution of Mn ions may reduce the life characteristics of a secondary battery.
In contrast, since the cathode active material according to the embodiment of the present invention may include structurally stable polycrystalline lithium manganese oxide having particles in a curved round shape by blunting the edges (corner portions) of the lithium manganese oxide, the cathode active material may address the limitations, such as the Jahn-Teller distortion and the dissolution of Mn2+. Thus, the life characteristics, and charge and discharge capacity characteristics of a secondary battery may be improved.
Also, since the boron-containing coating layer may be included on the surface of the polycrystalline lithium manganese oxide, tap density may increase, rolling density may increase, and the direct contact between the polycrystalline lithium manganese oxide and an electrolyte solution may be prevented to suppress side reactions between the cathode active material and the electrolyte solution.
In the cathode active material according to the embodiment of the present invention, the polycrystalline lithium manganese oxide may be represented by Chemical Formula 1:

Li(1+x)Mn(2−x−y)AlyO(4−z)  <Chemical Formula 1>

where x, y, and z respectively satisfy 0≦x≦0.2, 0<y≦0.2, and 0≦z≦0.2.
In the cathode active material according to the embodiment of the present invention, the polycrystalline lithium manganese oxide has a form in which a part of manganese sites in a spinel lithium manganese oxide is substituted with aluminum (Al).
In the polycrystalline lithium manganese oxide particles according to an embodiment of the present invention, the term “polycrystal” denotes a crystal composed of two or more crystal particles having an average crystal diameter of 152 nm to 300 nm, preferably 155 nm to 250 nm, and most preferably 150 nm to 210 nm.
Also, in the present specification, the crystal particles constituting the polycrystal may denote primary particles. The polycrystal may denote a form of a secondary particle in which the primary particles are agglomerated, and may be a spherical or nearly spherical polycrystal.
Also, in the cathode active material according to the embodiment of the present invention, the boron-containing coating layer may include a lithium boron oxide, a boron oxide, or a mixture thereof.
The boron-containing coating layer may act as a protective layer that prevents the direct contact between the cathode active material and the electrolyte solution, and may increase tap density by forming a coating layer on the lithium manganese oxide particles to obtain high rolling density. Thus, the boron-containing coating layer may be advantageous in the field of secondary batteries, particularly, vehicles. In particular, since an amount of lithium remaining on the surface of the cathode active material may be reduced by including lithium boron oxide in the boron-containing coating layer, a swelling phenomenon of the secondary battery may be reduced and the life characteristics thereof may be improved.
Specifically, the lithium boron oxide may include LiaBbOd (1≦a≦4, 1≦b≦4, and 1≦d≦8), and the boron oxide may include BxOy (1≦x≦4 and 1≦y≦4). For example, the boron-containing coating layer may include any one selected from the group consisting of Li2B4O7, LiBO3, and B2O3, or a mixture of two or more thereof.
Also, according to an embodiment of the present invention, the boron-containing coating layer may further include a reactant formed from the lithium boron oxide and the boron oxide.
According to an embodiment of the present invention, the boron-containing coating layer may include a mixed oxide of the lithium boron oxide and the boron oxide, and in this case, a content ratio of the lithium boron oxide to the boron oxide may be in a range of 1:1 to 1:4 as a weight ratio.
In the cathode active material according to the embodiment of the present invention, a thickness of the boron-containing coating layer may be in a range of 1 nm to 500 nm, and an amount of the lithium boron oxide, the boron oxide, and the mixture thereof included in the coating layer may be in a range of 0.01 wt % to about 20 wt % based on a total weight of the cathode active material.
In the case that the thickness of the coating layer is less than 1 nm, since the coating layer formed on the surface of the polycrystalline lithium manganese oxide is excessively thin, an effect of suppressing the side reactions between the cathode active material and the electrolyte solution may be insignificant. In the case in which the thickness of the coating layer is greater than 500 nm, since the coating layer is excessively thick, electrochemical properties may be reduced due to an increase in resistance.
Also, according to an embodiment of the present invention, the lithium manganese oxide may be doped with some boron (B) atoms of boron-containing oxide, and the lithium manganese oxide may have a concentration gradient in which an amount of the B gradually decreases from the surface of the lithium manganese oxide to the inside thereof.
In the cathode active material according to the embodiment of the present invention, an average particle diameter (D50) of a secondary particle, in which primary particles of the polycrystalline lithium manganese oxide are agglomerated, may be in a range of 3 μm to 20 μm. In the case that the average particle diameter of the secondary particle is less than 3 μm, the stability of the polycrystalline lithium manganese oxide particles may be reduced, and in the case in which the average particle diameter of the secondary particle is greater than 20 μm, the output characteristics of the secondary battery may be reduced.
In the present invention, the average particle diameter (D50) of the particles may be defined as a particle diameter at 50% in a cumulative particle diameter distribution. The average particle diameter (D50) of the particles according to the embodiment of the present invention, for example, may be measured by using a laser diffraction method. The laser diffraction method may generally measure a particle diameter ranging from a submicron level to a few mm, and may obtain highly repeatable and high resolution results.
A method of measuring the average particle diameter (D50) of particles according to an embodiment of the present invention, for example, may be performed in such a manner that the polycrystalline lithium manganese oxide particles or the cathode active material is dispersed in a solution, the solution is introduced into a commercial laser diffraction particle size measurement instrument (e.g., Microtrac MT 3000) and irradiated with ultrasonic waves having a frequency of about 28 kHz and an output of 60 W, and the average particle diameter (D50) at 50% in a cumulative particle diameter distribution of the measurement instrument may then be calculated.
Also, the cathode active material according to the embodiment of the present invention may have an effect of reducing the frictional area of the surface by including the boron-containing coating layer on the surface of the polycrystalline lithium manganese oxide, and thus, the tap density of the cathode active material may be improved.
The tap density may be in a range of 1.7 g/cc to 2.5 g/cc, wherein the tap density may vary according to the secondary particle diameter of the polycrystalline lithium manganese oxide.
Furthermore, according to an embodiment of the present invention, an average crystal diameter of the primary particles of the cathode active material may be quantitatively analyzed using X-ray diffraction analysis. For example, the cathode active material is put in a holder and diffraction data obtained by irradiating the particles with X-ray are analyzed so that the average crystal diameter of the primary particles may be quantitatively analyzed.
In X-ray diffraction analysis of the cathode active material according to the present invention, the cathode active material may have a structure in which (311), (400), and (440) planes are particularly grown with respect to a (111) plane.
Specifically, when a peak intensity ratio of I(111)/I(111) is defined as 100% in the X-ray diffraction analysis, I(311)/I(111) may be 40% or more, I(400)/I(111) may be 40% or more, and I(440)/I(111) may be 20% or more.
Also, according to an embodiment of the present invention, a full width at half maximum (FWHM) of a (311) peak of the cathode active material in X-ray diffraction analysis may be 0.3 degrees or less.
In the present invention, the FWHM quantifies a peak width at a half position of the (311) peak intensity which is obtained by the X-ray diffraction of the cathode active material.
The FWHM may be represented as degrees (°), i.e., the unit of 2θ, and the higher the crystallinity of the polycrystalline lithium manganese oxide particles is, the lower the value of the FWHM is.
Also, a Brunauer-Emmett-Teller (BET) specific surface area of the cathode active material according to the embodiment of the present invention may be in a range of 0.1 m2/g to 1.0 m2/g. In the case that the BET specific surface area is outside the above range, the output characteristics of the secondary battery may be reduced.
According to an embodiment of the present invention, the specific surface area of the cathode active material may be measured by a BET method. For example, the specific surface area may be measured by a 6-point BET method according to a nitrogen gas adsorption-flow method using a porosimetry analyzer (Belsorp-II mini by Bell Japan Inc.).
The present invention may provide a method of preparing the cathode active material, and for example, the cathode active material may be prepared by two methods. That is, there are a method (first preparation method) of mixing a manganese precursor coated with a boron-containing compound and a lithium precursor, and then sintering the mixture, and a method (second preparation method) of mixing a manganese precursor, a boron precursor, and a lithium precursor together, and sintering the mixture.
Specifically, the first preparation method of the cathode active material according to an embodiment of the present invention may include: (i) coating a surface of a polycrystalline manganese precursor with a boron-containing compound by mixing the polycrystalline manganese precursor and a boron precursor and performing a heat treatment; and (ii) forming a boron-containing coating layer on a surface of polycrystalline lithium manganese oxide by mixing the manganese precursor coated with the boron-containing compound and a lithium precursor and sintering the mixture.
Also, the second preparation method of the cathode active material according to another embodiment of the present invention may provide a method of preparing the cathode active material including mixing a polycrystalline manganese precursor, a boron precursor, and a lithium precursor, and sintering the mixture.
According to an embodiment of the present invention, crystals of the polycrystalline lithium manganese oxide may be easily grown at low temperature and the surface of the polycrystalline lithium manganese oxide may be uniformly coated with a boron-containing coating layer.
The boron precursor used according to the embodiment of the present invention may be used for the formation of the surface coating layer of the polycrystalline lithium manganese oxide, and simultaneously, may reduce a dissolution area of manganese by forming edges (corner portions) of the polycrystalline lithium manganese oxide particles into a curved round shape by blunting the edges thereof.
In the first preparation method according to the embodiment of the present invention, step (i) may be a step of coating the surface of the polycrystalline manganese precursor with the boron-containing compound by mixing the polycrystalline manganese precursor and the boron precursor and performing a heat treatment.
According to an embodiment of the present invention, the preparation method may further include performing a solid-liquid separation process before the heat treatment.
Specifically, the coating may be performed by wet mixing a polycrystalline manganese precursor with a boron precursor dissolved in a polar solvent to perform a solid-liquid separation process, and then drying the mixture by a heat treatment.
Any one selected from the group consisting of boric acid, lithium tetraborate, boron oxide, and ammonium borate, or a mixture of two or more thereof may be used as the boron precursor used according to the embodiment of the present invention. The boron precursor may be used in an amount of 0.01 wt % to 20 wt % based on a total weight of the polycrystalline manganese precursor.
Water, ethanol, acetone, or a mixed solvent thereof may be used as the polar solvent, and the boron precursor may be dissolved in the polar solvent, for example, ethanol, and may then be mixed with the manganese precursor.
The solid-liquid separation process used according to the embodiment of the present invention is a process used for the purpose of removing sulfur and sodium that remain on the surface of the precursors after mixing the precursors, and for example, the solid-liquid separation process may be performed by at least one method selected from the group consisting of centrifugal separation, filter press, filter drying, and spray drying methods.
After the centrifugal separation, a polycrystalline manganese precursor may be obtained in which the surface of the polycrystalline manganese precursor is coated with a boron-containing compound, for example, any one selected from the group consisting of B(OH)3, B2O3, H3BO3, B2O5, LiBO3, Li2B4O7, and Na2B4O7, or a mixture of two or more thereof, by heat treating in a temperature range of about 120° C. to about 300° C. for about 5 hours to about 48 hours.
In the case that the surface of the polycrystalline manganese precursor is uniformly coated with the boron-containing compound, the friction between the particles may be minimized and non-uniform particle growth may be controlled.
Thus, since the polycrystalline manganese oxide particles of the present invention obtained using the coated manganese precursor may have good crystallinity and may include a boron-containing coating layer on the particles, packing efficiency during rolling may be excellent.
In the preparation method according to the embodiment of the present invention, an average particle diameter (D50) of the polycrystalline manganese precursor may significantly affect the structural stability of the polycrystalline lithium manganese oxide particles and the performance characteristics of the secondary battery.
The polycrystalline manganese precursor usable according to an embodiment of the present invention may have the form of a polycrystal which is in the form of a secondary particle formed by the agglomeration of primary particles having an average crystal diameter of 100 nm to 300 nm, specifically 152 nm to 300 nm, preferably 155 nm to 250 nm, and most preferably 150 nm to 210 nm. In the polycrystalline manganese precursor, the definition of the term “polycrystal” may be the same as the definition in the polycrystalline lithium manganese oxide.
The average particle diameter (D50) of the secondary particle as the polycrystalline manganese precursor may be in a range of 3 μm to 20 μm, for example, 3 μm to 12 μm.
Also, in the manganese precursor according to the embodiment of the present invention, a fine and low-crystalline aluminum compound may exist in the state of being uniformly mixed with the manganese precursor. Al may be included in the manganese precursor in an amount of 0.01 wt % to 10 wt % based on the total weight of the manganese precursor. The polycrystalline manganese precursor including Al may include (Mn(1−y)Aly)3O4 (0<y≦0.2).
Specifically, the polycrystalline manganese precursor including Al may be formed by coprecipitating an aluminum compound and any one selected from the group consisting of MnO2, MnCl2, MnCO3, Mn3O4, MnSO4, and Mn2O3, or a mixture of two or more thereof using a coprecipitation method, and thus, the polycrystalline manganese precursor including Al may be obtained in the form of secondary particles in which two or more primary particles are agglomerated.
For example, distilled water and aqueous ammonia solution are put in a coprecipitation reactor and the mixture may then be stirred by supplying air into the reactor. Next, a manganese aluminum compound aqueous solution including any one selected from the group consisting of MnO2, MnCl2, MnCO3, Mn3O4, MnSO4, and Mn2O3, or a mixture of two or more thereof, and an aluminum compound (e.g., AlSO4) at an appropriate molar ratio, an aqueous ammonia solution as a complexing agent, and an alkaline aqueous solution as a pH adjuster are continuously added to the reactor and then mixed together. Then, a polycrystalline manganese compound (Mn(1−y)Aly)3O4 (0<y≦0.2, for example, 0<y≦0.1) containing Al may be prepared by introducing N2 into the reactor.
The aluminum compound may include any one selected from the group consisting of AlSO4, AlCl, and AlNO3, or a mixture of two or more thereof, but the present invention is not limited thereto.
In the first preparation method of the cathode active material according to the embodiment of the present invention, step (ii) may include mixing the manganese precursor coated with the boron-containing compound and the lithium precursor and sintering the mixture.
The sintering, for example, may be performed in a temperature range of 600° C. to 900° C. for about 2 hours to about 12 hours.
The lithium precursor may be any one selected from the group consisting of lithium chloride (LiCl), lithium carbonate (LiCO3), lithium hydroxide (LiOH), lithium phosphate (Li3PO4), and lithium nitrate (LiNO3), or a mixture of two or more thereof.
The second preparation method of the cathode active material according to another embodiment of the present invention may include mixing the polycrystalline manganese precursor, the boron precursor, and the lithium precursor, and heat treating the mixture.
The precursors used in the second preparation method may be the same as the precursors used in the first preparation method. The heat treatment may be performed in a temperature range of about 600° C. to less than about 800° C.
According to an embodiment of the present invention, in the case that the heat treatment is performed at a high temperature in the above temperature range, the polycrystalline lithium manganese oxide may be doped with some B atoms of the boron-containing coating layer.
Also, the present invention provides a cathode including the cathode active material.
The cathode may be prepared according to a typical method known in the art. For example, a binder, a conductive agent, and a dispersant, if necessary, as well as a solvent are mixed with a cathode active material and stirred to prepare a slurry, and a metal current collector is then coated with the slurry and pressed. Thereafter, the cathode may be prepared by drying the metal current collector.
Any metal may be used as the metal current collector so long as it is a metal having high conductivity as well as no reactivity in a voltage range of the battery to which the slurry of the electrode active material may be easily adhered. Non-limiting examples of the cathode current collector may include aluminum, nickel, or a foil prepared by a combination thereof.
An organic solvent, such as N-methylpyrrolidone (NMP), dimethylformamide (DMF), acetone, and dimethylacetamide, or water may be used as the solvent for forming the cathode. These solvents may be used alone or in a mixture of two or more thereof. An amount of the solvent used may be sufficient if the solvent may dissolve and disperse the cathode active material, the binder, and the conductive agent in consideration of a coating thickness of the slurry and manufacturing yield.
Various types of binder polymers, such as a polyvinylidene fluoride-hexafluoropropylene copolymer (PVDF-co-HEP), polyvinylidene fluoride, polyacrylonitrile, polymethylmethacrylate, polyvinyl alcohol, carboxymethyl cellulose (CMC), starch, hydroxypropyl cellulose, regenerated cellulose, polyvinylpyrrolidone, tetrafluoroethylene, polyethylene, polypropylene, polyacrylate, an ethylene-propylene-diene monomer (EPDM), a sulfonated EPDM, a styrene-butadiene rubber (SBR), a fluorine rubber, poly(acrylic acid), polymers in which hydrogens thereof are substituted with lithium (Li), sodium (Na), or calcium (Ca), or various copolymers, may be used as the binder.
Any conductive agent may be used without particular limitation so long as it has suitable conductivity without causing adverse chemical changes in the batteries. For example, the conductive agent may include a conductive material such as: graphite such as natural graphite and artificial graphite; carbon black such as acetylene black, Ketjen black, channel black, furnace black, lamp black, and thermal black; conductive fibers such as carbon fibers and metal fibers; conductive tubes such as carbon nanotubes; metal powder such as fluorocarbon powder, aluminum powder, and nickel powder; conductive whiskers such as zinc oxide whiskers and potassium titanate whiskers; conductive metal oxide such as titanium oxide; or polyphenylene derivatives.
An aqueous-based dispersant or an organic dispersant, such as N-methyl-2-pyrrolidone, may be used as the dispersant.
Also, the present invention provides a secondary battery including the cathode, an anode, and a separator disposed between the cathode and the anode.
A carbon material, lithium metal, silicon, or tin, which may intercalate and deintercalate lithium ions, may be typically used as an anode active material that is used in the anode according to an embodiment of the present invention. For example, the carbon material may be used and both low crystalline carbon and high crystalline carbon may be used as the carbon material. Typical examples of the low crystalline carbon may be soft carbon and hard carbon, and typical examples of the high crystalline carbon may be natural graphite, Kish graphite, pyrolytic carbon, mesophase pitch-based carbon fibers, meso-carbon microbeads, mesophase pitches, and high-temperature sintered carbon such as petroleum or coal tar pitch derived cokes.
Furthermore, the anode collector is generally fabricated to have a thickness of 3 μm to 500 μm. The anode collector is not particularly limited so long as it has conductivity without causing adverse chemical changes in the batteries. The anode collector may be formed of, for example, copper, stainless steel, aluminum, nickel, titanium, fired carbon, copper or stainless steel that is surface-treated with one of carbon, nickel, titanium, silver, or the like, an aluminum-cadmium alloy, or the like. Also, like the cathode collector, the anode collector may have a fine roughness surface to improve bonding strength of an anode active material. The anode collector may have various shapes such as a film, a sheet, a foil, a net, a porous body, a foam body, a non-woven fabric body, and the like.
Similar to the cathode, a binder and a conductive agent, which are typically used in the art, may be used in the anode. An anode active material and the above additives are mixed and stirred to prepare an anode active material slurry. Then, a current collector is coated therewith and pressed to prepare the anode.
Also, a typical porous polymer film used as a typical separator, for example, a porous polymer film prepared from a polyolefin-based polymer, such as an ethylene homopolymer, a propylene homopolymer, an ethylene/butene copolymer, an ethylene/hexene copolymer, and an ethylene/methacrylate copolymer, may be used alone or in a lamination therewith as the separator. Also, a typical porous nonwoven fabric, for example, a nonwoven fabric formed of high melting point glass fibers or polyethylene terephthalate fibers may be used. However, the present invention is not limited thereto.
A lithium salt, which may be included as the electrolyte used in the present invention, may be used without limitation so long as it is typically used in an electrolyte for a lithium secondary battery. For example, any one selected from the group consisting of F−, Cl−, Br−, I−, NO3−, N(CN)2−, BF4−, ClO4−, PF6−, (CF3)2PF4−, (CF3)3PF3−, (CF3)4PF2−, CF3)5PF−, (CF3)6P−, CF3SO3−, CF3CF2SO3−, (CF3SO2)2N−, (FSO2)2N−, CF3CF2(CF3)2CO−, (CF3SO2)2CH−, (SF5)3C−, (CF3SO2)3C−, CF3(CF2)7SO3−, CF3CO2−, CH3CO2−, SCN−, and (CF3CF2SO2)2N− may be used as an anion of the lithium salt.
The electrolyte used in the present invention may include an organic liquid electrolyte, an inorganic liquid electrolyte, a solid polymer electrolyte, a gel-type polymer electrolyte, a solid inorganic electrolyte, and a molten inorganic electrolyte, which may be used in the preparation of a lithium secondary battery. However, the present invention is not limited thereto.
A shape of the lithium secondary battery of the present invention is not particularly limited, and for example, a cylindrical type using a can, a prismatic type, a pouch type, or a coin type may be used.
The lithium secondary battery according to the present invention may not only be used in a battery cell that is used as a power source of a small device, but may also be used as a unit cell in a medium and large sized battery module including a plurality of battery cells.
Preferred examples of the medium and large sized device may be an electric vehicle, a hybrid electric vehicle, a plug-in hybrid electric vehicle, or a power storage system, but the medium and large sized device is not limited thereto.
Hereinafter, the present invention will be described in detail, according to specific examples. The invention may, however, be embodied in many different forms and should not be construed as being limited to the embodiments set forth herein. Rather, these example embodiments are provided so that this description will be thorough and complete, and will fully convey the scope of the present invention to those skilled in the art.
EXAMPLES
Hereinafter, the present invention will be described in more detail, according to examples and experimental examples. However, the present invention is not limited thereto.
Preparation Example 1: Preparation of Al-Containing Polycrystalline Manganese Precursor
MnSO4 and AlSO4 were mixed at a ratio of 98:2, and MnSO4.7H2O including 2M AlSO4 was then prepared using distilled water subjected to N2 purging. The prepared MnSO4.7H2O was introduced into a continuous stirred tank reactor (CSTR, CSTR-L0, EMS Tech) at a rate of 250 mL/h.
A pH value of the solution was maintained to be 10.5 using a pH meter and a controller while introducing an 40% sodium hydroxide aqueous solution as an alkalizing agent at a rate of 230 mL/h to 250 mL/h through a sodium hydroxide aqueous solution supply unit of the reactor and a 25% ammonia solution at a rate of 30 mL/h through an ammonia solution supply unit of the reactor. A temperature of the reactor was set to be 40° C., a retention time (RT) was controlled to be 10 hours, and stirring was performed at a speed of 1,200 rpm to precipitate as Mn3O4 including Al.
The reaction solution thus obtained was filtered through a filter and purified with distilled water. Then, an additional process of drying was performed to prepare (Mn0.95Al0.05)3O4 including Al. The (Mn0.95Al0.05)3O4 was in the form of secondary particles in which two or more primary particles were agglomerated, had an average particle diameter of 5 μm, and contained about 2.1 wt % of Al.
Preparation of Polycrystalline Lithium Manganese Oxide Particles
Example 1
Step (i): Obtaining Polycrystalline Manganese Precursor Coated with Boron-Containing Compound
0.62 g of boric acid was dissolved in 1 L of ethanol, and both the solution thus prepared and 141.88 g of the (Mn0.95Al0.05)3O4 having an average particle diameter of 5 μm prepared in Preparation Example 1 were then put in a 1 L bottle and stirred at 400 rpm for 1 hour. The mixed solution thus obtained was centrifuged and then dried at 150° C. for 24 hours to obtain polycrystalline manganese precursor coated with a boron-containing compound (B(OH)3).
Step (ii): Obtaining Cathode Active Material Having Boron-Containing Coating Layer on the Surface Thereof
135 g of the polycrystalline manganese precursor coated with a boron-containing compound (B(OH)3) obtained in step (i) and 37.50 g of Li2CO3 as a lithium precursor were put in a mixer (Waring blender) and mixed at a speed of the center of the mixer of 18,000 rpm for 1 minute to obtain a precursor mixture.
The precursor mixture thus obtained was put in a 500 cc alumina crucible and sintered at about 800° C. for 4 hours in an air atmosphere.
A cake obtained after the sintering was ground in a mortar and then classified using a 400 mesh sieve to obtain Li1.09Mn1.81Al0.1O4 having a coating layer including Li2B4O7, LiBO3, and B2O3 on the surface thereof.
The Li1.09Mn1.81Al0.1O4 having a coating layer was secondary particles composed of two or more crystal particles (primary particles) having an average crystal diameter of 160 nm, wherein an average particle diameter of the secondary particle was 10 μm. Also, a thickness of the coating layer was 100 nm.
Example 2
37.50 g of Li2CO3, 141.88 g of (Mn0.95Al0.05)3O4 having an average particle diameter of 5 μm prepared in Preparation Example 1, 0.62 g of boric acid were put in a mixer (Waring blender) and mixed at a speed of the center of the mixer of 18,000 rpm for 1 minute. The mixed powder was put in a 500 cc alumina crucible and sintered at about 700° C. for 4 hours in an air atmosphere. A cake obtained after the sintering was ground in a mortar and then classified using a 400 mesh sieve to obtain Li1.09Mn1.81Al0.1O4 having a coating layer including Li2B4O7, LiBO3, and B2O3 on the surface thereof.
The Li1.09Mn1.81Al0.1O4 having a coating layer was secondary particles composed of two or more crystal particles (primary particles) having a crystal diameter of 178 nm, wherein an average particle diameter of the secondary particle was 9.5 μm. Also, a thickness of the coating layer was 100 nm.
Comparative Example 1
Li1.09Mn1.81Al0.1O4 was obtained in the same manner as in Example 1 except that step (i) of Example 1 was not performed and an uncoated polycrystalline manganese precursor was used in step (ii) instead of using a polycrystalline manganese precursor coated with a boron-containing compound.
Comparative Example 2
LiMn2O4 having a coating layer including Li2B4O7, LiBO3, and B2O3 was obtained in the same manner as in Example 1 except that single crystal Mn3O4 was used as a manganese precursor instead of using the polycrystalline (Mn0.95Al0.05)3O4 prepared in Preparation Example 1.
The LiMn2O4 having a coating layer was a single crystal, wherein the particle diameter thereof was in a range of 5 μm to 10 μm. Also, a thickness of the coating layer was 100 nm.
Preparation of Lithium Secondary Battery
Example 3
Cathode Preparation
A cathode mixture slurry was prepared by adding 94 wt % of the cathode active material prepared in Example 1, 3 wt % of carbon black as a conductive agent, and 3 wt % of polyvinylidene fluoride (PVdF) as a binder to N-methyl-2-pyrrolidone (NMP) as a solvent. An about 20 μm thick aluminum (Al) thin film as a cathode collector was coated with the cathode mixture slurry and dried, and the Al thin film was then roll-pressed to prepare a cathode.
Anode Preparation
An anode active material slurry was prepared by mixing 96.3 wt % of carbon powder as an anode active material, 1.0 wt % of super-p as a conductive agent, and 1.5 wt % of styrene-butadiene rubber (SBR) and 1.2 wt % of carboxymethyl cellulose (CMC) as a binder, and adding the mixture to NMP as a solvent. A 10 μm thick copper (Cu) thin film as an anode collector was coated with the anode active material slurry and dried, and the Cu thin film was then roll-pressed to prepare an anode.
Non-Aqueous Electrolyte Solution Preparation
A 1 M LiPF6 non-aqueous electrolyte solution was prepared by adding LiPF6 to a non-aqueous electrolyte solvent that was prepared by mixing ethylene carbonate and diethyl carbonate, as an electrolyte, at a volume ratio of 30:70.
Lithium Secondary Battery Preparation
A mixed separator of polyethylene and polypropylene was disposed between the cathode and anode thus prepared, and a polymer type battery was then prepared by a typical method. Then, the preparation of each lithium secondary battery was completed by injecting the prepared non-aqueous electrolyte solution.
Example 4
A lithium secondary battery was prepared in the same manner as in Example 3 except that the cathode active material prepared in Example 2 was used.
Comparative Examples 3 and 4
Lithium secondary batteries were prepared in the same manner as in Example 3 except that the cathode active materials prepared in Comparative Examples 1 and 2 were respectively used.
Experimental Example 1: Scanning Electron Microscope (SEM) Image
SEM images were respectively obtained from the cathode active materials prepared in Examples 1 and 2 and Comparative Examples 1 and 2, and the results thereof are presented in FIGS. 2 to 5, respectively.
Specifically, as illustrated in FIGS. 2 and 3, it may be identified that the cathode active materials prepared according to Examples 1 and 2 of the present invention had a boron-containing coating layer on the surface of the polycrystalline lithium manganese oxide and had curved round edges (corners).
In contrast, as illustrated in FIG. 4 which illustrates an SEM image of the cathode active material of Comparative Example 1, with respect to the surface of the cathode active material using the polycrystalline manganese precursor on which a boron-containing compound was not coated, it was observed that particles had sharper edges (corners) than particles of FIGS. 2 and 3. In this case, it may be estimated that the dissolution of manganese may occur due to the sharp edges of the particles.
Also, as illustrated in FIG. 5 which illustrates a surface SEM image of LiMn2O4 having a coating layer in which the single crystal manganese precursor was used as in Comparative Example 2, particles had round edges (corners) due to the use of a sintering aid, but it may be understood that the shape and size of the particles were non-uniform and, different from the SEM images of FIGS. 2 and 3, the particles were in the form of primary particles instead of the form of secondary particles in which primary particles were agglomerated.
Experimental Example 2: X-Ray Diffraction Analysis
X-ray diffraction analysis was performed on the polycrystalline lithium manganese oxide particles prepared in Examples 1 and 2 and Comparative Examples 1 and 2. The results thereof are presented in Table 1 below.












TABLE 1







(111)/(111)
(311)/(111)
(400)/(111)
(440)/(111)




















Example 1
100.0
47.8
46.9
29.2


Example 2
100.0
46.1
45.5
28.1


Comparative
100.0
31.1
13.5
14.5


Example 1


Comparative
100.0
38.6
37.7
23.2


Example 2









As illustrated in Table 1, in the X-ray diffraction analysis of the cathode active materials prepared in Examples and 2, it may be identified that the cathode active materials may have a structure, in which (311), (400), and (440) planes were particularly grown with respect to a (111) plane, in comparison to Comparative Examples 1 and 2.
Specifically, with respect to the cathode active materials of Examples 1 and 2, when the peak intensity ratio of I(111)/I(111) was determined as 100% in the X-ray diffraction analysis, I(311)/I(111) was 46% or more, I(400)/I(111) was 46% or more, and I(440)/I(111) was 28% or more.
In contrast, with respect to Comparative Example 1, when the peak intensity ratio of I(111)/I(111) was determined as 100%, I(311)/I(111) was about 31.1%, I(400)/I(111) was about 13.5%, and I(440)/I(111) was about 14.5%, and thus, it may be confirmed that crystallinity was significantly decreased in comparison to Examples 1 and 2. In particular, it may be confirmed that the peak intensity ratios of I(400)/I(111) of Examples 1 and 2 were significantly increased by 3 times or more that of Comparative Example 1.
Similarly, with respect to Comparative Examples 2, when the peak intensity ratio of I(111)/I(111) was determined as 100%, I(311)/I(111) was about 38%, I(400)/I(111) was about 37.7%, and I(440)/I(111) was about 23.2%, and thus, it may be confirmed that crystallinity was decreased by 20% or more in comparison to Examples 1 and 2.
Experimental Example 3: Electrochemical Experiments
The lithium secondary batteries (battery capacity: 3.4 mAh) prepared in Examples 3 and 4 and Comparative Examples 3 and 4 were charged at a constant current (CC) of 2 C under constant current/constant voltage (CC/CV) conditions, and thereafter, charge in the first cycle was performed by charging the lithium secondary batteries at a constant voltage (CV) to a current of 0.17 mAh. After the batteries were left standing for 20 minutes, discharge capacities in the first cycle were measured by discharging the batteries at a constant current of 0.1 C to a voltage of 10 mV. Subsequently, with respect to each battery, the charge and discharge were repeated to measure capacity, and the results thereof are presented in Table 2 below.











TABLE 2








Comparative
Comparative


Category
Example 3
Example 4
Example 3
Example 4



















Charge
106.26
107.5
85.4
105.9


capacity


[mAh/g]


Discharge
104.81
105.4
84.4
103.5


capacity


[mAh/g]


1st
98.63
98.05
98.8
97.7


efficiency


[%]


C-rate
99.62
99.15
99.4
98.8


[2.0 C/0.1 C]









As illustrated in Table 2, it may be confirmed that the lithium secondary batteries of Examples 3 and 4, in which the cathode active materials having a boron-containing coating layer on the surface thereof were used, had better charge and discharge capacity characteristics and efficiency characteristics than Comparative Example 3, in which the cathode active material not having a boron-containing coating layer on the surface thereof was used, and Comparative Example 4 using the LiMn2O4 cathode active material having a coating layer.
That is, with respect to the lithium secondary batteries of Examples 3 and 4, charge and discharge capacities were improved by about 20% in comparison to the lithium secondary battery of Comparative Example 3 and were improved by about 1% in comparison to the lithium secondary battery of Comparative Example 4.
Also, initial efficiency and output characteristics of the lithium secondary batteries of Examples 3 and 4 were improved by about 0.5% to about 0.9% in comparison to those of the lithium secondary batteries of Comparative Examples 3 and 4.
Experimental Example 4: Tap Density Measurement
The cathode active materials obtained in Example 1 and Comparative Examples 1 and 2 were respectively charged into a container and, as a tap density of each cathode active material, an apparent density of particles was measured by vibrating under a predetermined condition.
Tap densities were respectively measured on the cathode active material having a boron-containing coating layer on the surface of the polycrystalline lithium manganese oxide of Example 1, the cathode active material of Comparative Example 1 in which the coating layer is not included, and the cathode active material having a boron-containing coating layer on the surface of the single crystal lithium manganese oxide of Comparative Example 2. The results of the tap densities are presented in Table 3 below.









TABLE 3







Tap density (g/cc)



















Example 1
1.9



Comparative Example 1
1.6



Comparative Example 2
1.8










As illustrated in Table 3, with respect to the cathode active material having a boron-containing coating layer on the surface thereof of Example 1, it may be understood that the tap density was improved in comparison to the cathode active material not having a boron-containing coating layer on the surface thereof of Comparative Example 1 and the LiMn2O4 cathode active material having a coating layer of Comparative Example 2.
Specifically, in the case that the surface of the polycrystalline manganese precursor was uniformly coated with a boron-containing compound, the friction between particles may be minimized and non-uniform particle growth may be controlled.
Thus, since the polycrystalline manganese oxide particles of the present invention obtained using the coated manganese precursor may have good crystallinity and may include a boron-containing coating layer on the particles, the packing efficiency during rolling may be excellent.
In contrast, with respect to Comparative Examples 1 and 2, different from Example 1, it may be understood that the tap densities were decreased because an amount of non-uniform particles was increased.
Experimental Example 5: Crystal Size Measurement
Crystal diameters of the cathode active materials of Examples 1 and 2 and Comparative Example 1 were measured.
Specifically, about 5 g of the cathode active materials of Examples 1 and 2 and Comparative Example 1 were respectively put in a holder and the crystal diameter may be calculated by analyzing diffraction data obtained by irradiating each cathode active material with X-ray.
The crystal diameter may be calculated from a full width at half maximum of a main peak or three or more peaks, and the crystal diameter may correspond to an average crystal diameter of the primary particles of the polycrystalline lithium manganese oxide particles. The average crystal diameters of the primary particles of the polycrystalline lithium manganese oxide particles according to the above results are presented in Table 4 below.












TABLE 4










Comparative



Category
Example 1
Example 2
Example 1





















Crystal
160
178
143



diameter (nm)










As illustrated in Table 4, the average crystal diameters of the cathode active materials having a boron-containing coating layer on the surface thereof of Examples 1 and 2 were in a range of 160 nm to 178 nm, but the average particle diameter of the cathode active material not having a boron-containing coating layer on the surface thereof of Comparative Example 1 was 143 nm.
From the above results, it may be understood that the crystal diameter may increase depending on whether the boron-containing coating layer was included or not.
INDUSTRIAL APPLICABILITY
In the case that a cathode active material according to an embodiment of the present invention is used in a lithium secondary battery, the cathode active material may suppress side reactions between the cathode active material and an electrolyte solution by preventing direct contact between polycrystalline lithium manganese oxide and the electrolyte solution, and may improve tap density, life characteristics, and charge and discharge capacity characteristics of the secondary battery.

## Claims

1. A cathode active material comprising:
polycrystalline lithium manganese oxide; and
a boron-containing coating layer on a surface of the polycrystalline lithium manganese oxide, and wherein the polycrystalline lithium manganese oxide particles are in a form of secondary particles in which two or more primary particles having an average crystal diameter of 152 nm to 300 nm are agglomerated.

2. The cathode active material of claim 1, wherein the polycrystalline lithium manganese oxide is represented by Chemical Formula 1:


Li(1+x)Mn(2−x−y)AlyO(4−z)  <Chemical Formula 1>

where x, y, and z respectively satisfy 0≦x≦0.2, 0<y≦0.2, and 0≦z≦0.2.

3. The cathode active material of claim 1, wherein the boron-containing coating layer comprises a lithium boron oxide, a boron oxide, or a mixture thereof.

4. The cathode active material of claim 3, wherein the lithium boron oxide comprises LiaBbOd (1≦a≦4, 1≦b≦4, and 1≦d≦8), and the boron oxide comprises BxOy (1≦x≦4 and 1≦y≦4).

5. The cathode active material of claim 1, wherein the boron-containing coating layer comprises any one selected from the group consisting of Li2B4O7, LiBO3, and B2O3, or a mixture of two or more thereof.

6. The cathode active material of claim 5, wherein the boron-containing coating layer further comprises a reactant formed by a reaction of the lithium boron oxide and the boron oxide.

7. The cathode active material of claim 4, wherein the boron-containing coating layer comprises a mixed oxide of the lithium boron oxide and the boron oxide in a weight ratio of the lithium boron oxide to the boron oxide of 1:1 to 1:4.

8. The cathode active material of claim 1, wherein a thickness of the boron-containing coating layer is in a range of 1 nm to 500 nm.

9. The cathode active material of claim 1, wherein an average particle diameter (D50) of the secondary particle is in a range of 3 μm to 20 μm.

10. The cathode active material of claim 1, wherein a tap density of the cathode active material is in a range of 1.7 g/cc to 2.5 g/cc.

11. The cathode active material of claim 1, wherein I(311)/I(111) of the cathode active material is 40% or more when a peak intensity ratio of I(111)/I(111) is defined as 100% in X-ray diffraction analysis.

12. The cathode active material of claim 1, wherein I(400)/I(111) and I(440)/I(111) of the cathode active material are respectively 40% or more and 20% or more when a peak intensity ratio of I(111)/I(111) is defined as 100% in X-ray diffraction analysis.

13. The cathode active material of claim 1, wherein a full width at half maximum (FWHM) of a (311) peak of the cathode active material in X-ray diffraction analysis is 0.3 degrees or less.

14. The cathode active material of claim 1, wherein a Brunauer-Emmett-Teller (BET) specific surface area of the cathode active material is in a range of 0.1 m2/g to 1.0 m2/g.

15. The cathode active material of claim 1, wherein the lithium manganese oxide is doped with at least one boron (B) atom of boron-containing oxide, and the lithium manganese oxide has a concentration gradient in which an amount of the B decreases from the surface of the lithium manganese oxide to inside thereof.

16. A method of preparing the cathode active material of claim 1 comprising:
(i) coating a surface of a polycrystalline manganese precursor with a boron-containing compound by mixing the polycrystalline manganese precursor and a boron precursor and performing a heat treatment; and
(ii) forming a boron-containing coating layer on a surface of polycrystalline lithium manganese oxide by mixing the manganese precursor coated with the boron-containing compound and a lithium precursor and sintering the mixture.

17. A method of preparing the cathode active material of claim 1 comprising mixing a polycrystalline manganese precursor, a boron precursor, and a lithium precursor, and sintering the mixture.

18. The method of claim 16, further comprising performing a solid-liquid separation process before the heat treatment.

19. The method of claim 18, wherein the solid-liquid separation process is performed by at least one method selected from the group consisting of centrifugal separation, filter press, filter drying, and spray drying methods.

20. The method of claim 16, wherein the polycrystalline manganese precursor is in a form of secondary particles in which two or more primary particles having an average crystal diameter of 100 nm to 300 nm are agglomerated.

21. The method of claim 16, wherein the polycrystalline manganese precursor comprises aluminum (Al) in an amount of 0.01 wt % to 10 wt %.

22. The method of claim 21, wherein the polycrystalline manganese precursor comprises (Mn(1−y)Aly)3O4 (0≦y≦0.2).

23. The method of claim 22, wherein the polycrystalline manganese precursor is formed by coprecipitating an aluminum compound and any one selected from the group consisting of MnO2, MnCl2, MnCO3, Mn3O4, MnSO4, and Mn2O3, or a mixture of two or more thereof.

24. The method of claim 23, wherein the aluminum compound comprises any one selected from the group consisting of AlSO4, AlCl, and AlNO3, or a mixture of two or more thereof.

25. The method of claim 16, wherein the boron precursor comprises any one selected from the group consisting of boric acid, lithium tetraborate, boron oxide, and ammonium borate, or a mixture of two or more thereof.

26. The method of claim 16, wherein the boron precursor is used in an amount of 0.01 wt % to 20 wt % based on a total weight of the polycrystalline manganese precursor.

27. The method of claim 16, wherein the boron-containing compound comprises any one selected from the group consisting of B(OH)3, B2O3, H3BO3, B2O5, LiBO3, Li2B4O7, and Na2B4O7, or a mixture of two or more thereof.

28. The method of claim 16, wherein the sintering is performed in a temperature range of 600° C. to 900° C.

29. The method of claim 18, wherein the sintering is performed in a temperature range of 600° C. to less than 800° C.

30. A cathode comprising the cathode active material of claim 1.

31. A lithium secondary battery comprising the cathode of claim 30.

32. The method of claim 17, wherein the polycrystalline manganese precursor is in a form of secondary particles in which two or more primary particles having an average crystal diameter of 100 nm to 300 nm are agglomerated.

33. The method of claim 17, wherein the polycrystalline manganese precursor comprises aluminum (Al) in an amount of 0.01 wt % to 10 wt %.

34. The method of claim 17, wherein the boron precursor comprises any one selected from the group consisting of boric acid, lithium tetraborate, boron oxide, and ammonium borate, or a mixture of two or more thereof.

35. The method of claim 17, wherein the boron precursor is used in an amount of 0.01 wt % to 20 wt % based on a total weight of the polycrystalline manganese precursor.