Patent Application
20230369571
The present disclosure relates to a cathode active material for a secondary battery, containing lithium composite oxide containing a layered structure of overlithiated oxide.
With the development of portable mobile electronic devices, such as a smartphone, an MP3 player, and a tablet PC, the demand for secondary batteries capable of storing electric energy is explosively increasing. In particular, with the advent of electric vehicles, medium and large energy storing systems, and portable devices requiring high energy density, the demand for lithium secondary batteries is increasing.
A material mostly favored recently as a cathode active material is a lithium-nickel-manganese-cobalt oxide, Li(NixCoyMnz)O2 (herein, x, y, and z are each independently an atomic fraction of oxide-composition elements, and 0<x≤1, 0<y≤1, 0<z≤1, and 0<x+y+z≤1). This material has the advantage of high capacity since the material is used at a higher voltage than LiCoO2 that has been actively studied and used as a cathode active material, and has the advantage of low price due to a relatively small Co content therein. However, this material has disadvantages of unsatisfactory rate capability and poor cycle life characteristics at high temperatures.
Hence, research has been conducted to apply overlithiated layered oxide, which exhibits higher reversible capacity than conventional Li(NixCoyMnz)O2, to a lithium secondary battery.
However, there are problems of decreased discharge capacity (cycle life) and voltage decay during life cycling, which is due to phase transition from a spinel-like structure to a cubic structure due to transition metal migration during life cycling. These decreased discharge capacity (cycle life) and voltage decay are problems that must be solved in order to realize practical application to a lithium secondary battery.
The present disclosure is intended to increase the charge/discharge capacity and solve the problems of life cycle deterioration and voltage decay by suppressing phase transition during life cycling in a cathode active material for a secondary battery.
Furthermore, the present disclosure is intended to increase the lithium ion mobility and improve the rate capability in a cathode active material for a secondary battery.
Furthermore, the present disclosure is intended to improve surface kinetic and structural stability of a cathode active material for a secondary battery.
The above problems are not solved by the following.
In accordance with an aspect of the present disclosure, there is provided a cathode active material for a secondary battery, including a lithium composite oxide represented by Formula 1 below and containing a layered structure of overlithiated oxide, wherein: the lithium composite oxide includes a secondary particle, the secondary particle includes at least one primary particle, and the primary particle includes at least one crystallite; at least one selected from the secondary particle, the primary particle, and the crystallite includes a core and a shell occupying at least a part of the surface of the core; and when the number of moles of at least one element selected from the group consisting nickel (Ni), cobalt (Co), and manganese (Mn) to the total number of moles of M1 and M2 in Formula 1 is NCM/M, the NCM/M in the shell is different than in the core of the secondary particle:
rLi2M1O3·(1−r)LiaM2O2 [Formula 1]
As a more preferable embodiment, the shell of the secondary particle may include a concentration gradient portion in which at least one element selected from nickel (Ni), cobalt (Co), and manganese (Mn) has a concentration gradient.
As a still more preferable embodiment, the shell of the primary particle may include a concentration gradient portion in which at least one element selected from nickel (Ni), cobalt (Co), and manganese (Mn) has a concentration gradient.
As a still more preferable embodiment, the shell of the crystallite may include a concentration gradient portion in which at least one element selected from nickel (Ni), cobalt (Co), and manganese (Mn) has a concentration gradient.
In the cathode active material for a secondary battery according to the present disclosure, the phase transition during life cycling is suppressed to increase the charge/discharge capacity and solve the problems of life cycle deterioration and voltage decay.
Furthermore, the cathode active material for a secondary battery according to the present disclosure has increased lithium ion mobility and improved rate capability.
Furthermore, the cathode active material for a secondary battery according to the present disclosure has improved surface kinetic and structural stability.
As used herein, terms such as “comprising” should be understood as open-ended terms that do not preclude the inclusion of other technical features.
As used herein, the terms “as an example”, “as an example”, and “preferably” refer to embodiments of the present disclosure that may afford certain benefits, under certain circumstances, and are not intended to exclude other embodiments from the scope of the disclosure.
A cathode active material for a secondary battery according to an embodiment of the present disclosure contains a lithium composite oxide represented by Formula 1 below and containing a layered structure of overlithiated oxide.
rLi2M1O3·(1−r)LiaM2O2 [Formula 1]
In Formula 1, 0<r<1 and 0<a≤1; M1 and M2 are each independent; M1 is at least one selected from Mo, Nb, Fe, Cr, V, Co, Cu, Zn, Sn, Mg, Ni, Ru, Al, Ti, Zr, B, Mn, Na, K, Y, P, Ba, Sr, La, Ga, Gd, Sm, W, Ca, Ce, Ta, Sc, In, S, Ge, Si, and Bi; and M2 is at least one selected from Mo, Nb, Fe, Cr, V, Co, Cu, Zn, Sn, Mg, Ni, Ru, Al, Ti, Zr, B, Mn, Na, K, Y, P, Ba, Sr, La, Ga, Gd, Sm, W, Ca, Ce, Ta, Sc, In, S, Ge, Si, and Bi.
As a preferable example, M1 is at least one selected from Mn, Cr, Fe, Co, Ni, Mo, Ru, W, Ti, Zr, Sn, V, Al, Mg, Ta, B, P, Nb, Cu, La, Ba, Sr, and Ce; and M2 is at least one selected from Ni, Co, Mn, Cr, Fe, Mo, Ru, W, Ti, Zr, Sn, V, Al, Mg, Ta, B, P, Nb, Cu, La, Ba, Sr, and Ce.
As an example, in Formula 1, the overlithiated oxide may be a solid solution phase in which monoclinic-structured Li2M1O3 and rhombohedral-structured LiaM2O2 are present in a mixed state.
As a more preferable example, the average valence of M1 may be 3.5 to 4.5 or may be 4.
As a more preferable example, the average valence of M2 may be 2.5 to 3.5 or may be 3.
As a preferable example, Formula 1 may be expressed as Formula 1-1 below.
rLi2MnpMd11−pO3·(1−r)LiaNixCoyMnzMd21−(x+y+z)O2 [Formula 1-1]
In Formula 1-1, 0<r<1, 0<p≤1, 0<a≤1, 0≤x≤1, 0≤y≤1, 0≤z≤1, and 0<x+y+z≤1; Md1 and Md2 are each independent; Md1 is at least one selected from Mo, Nb, Fe, Cr, V, Co, Cu, Zn, Sn, Mg, Ni, Ru, Al, Ti, Zr, B, Na, K, Y, P, Ba, Sr, La, Ga, Gd, Sm, W, Ca, Ce, Ta, Sc, In, S, Ge, Si, and Bi; and Md2 is at least one selected from Mo, Nb, Fe, Cr, V, Cu, Zn, Sn, Mg, Ru, Al, Ti, Zr, B, Na, K, Y, P, Ba, Sr, La, Ga, Gd, Sm, W, Ca, Ce, Ta, Sc, In, S, Ge, Si, and Bi.
Md1 and Md2 may be each independently an element, a dopant, or a coating material, and desired effects of the present disclosure can be obtained regardless of the types of Md1 and Md2.
As a more preferable example, Md1 is at least one selected from Cr, Fe, Co, Ni, Mo, Ru, W, Ti, Zr, Sn, V, Al, Mg, Ta, B, P, Nb, Cu, La, Ba, Sr, and Ce; and Md2 is at least one selected from Cr, Fe, Mo, Ru, W, Ti, Zr, Sn, V, Al, Mg, Ta, B, P, Nb, Cu, La, Ba, Sr, and Ce.
As an example, in Formula 1-1, the overlithiated oxide may be a solid solution phase in which monoclinic-structured Li2MnpMd11−pO3 and rhombohedral-structured LiaNixCoyMnzMd1−(x+y+z)O2 are present in a mixed state.
As an example, the overlithiated oxide may have a layered structure in which a lithium atomic layer alternately overlaps an atomic layer of nickel, cobalt, manganese, or Md via an oxygen atomic layer interposed therebetween.
As an example, r may be not greater than 1, not greater than 0.9, not greater than 0.8, not greater than 0.7, or not greater than 0.6.
As an example, p may be greater than 0, may be not smaller than 0.1, 0.2, 0.3, 0.4, 0.5, 0.6, 0.7, 0.8, or 0.9, or may be 1.0.
As a more preferable example, in the lithium composite oxide of the present disclosure, the number of moles of lithium to the total number of moles of M1 and M2, Li/M, may be not lower than 1.01, 1.05, or 1.1 and may be not higher than 1.7, 1.6, 1.5, 1.4, or 1.3.
As a more preferable example, in the lithium composite oxide, the number of moles of lithium (Li) to the total number of moles of M1 and M2, Li/M, may be not lower than 0.1, 0.2, or 0.3 and may be not higher than 0.7, 0.6, or 0.5.
As a more preferable example, in the lithium composite oxide, the number of moles of cobalt (Co) to the total number of moles of M1 and M2, Co/M, may be not lower than 0.0, 0.05, or 0.1 and may be not higher than 0.3, 0.2, or 0.1.
As a more preferable, a cathode active material according to an embodiment of the present disclosure may not contain Co.
As a more preferable example, in the lithium composite oxide, the number of moles of manganese (Mn) to the total number of moles of M1 and M2, Mn/M, may be not lower than 0.1, 0.2, or 0.3 and may be not higher than 0.8 or 0.7.
As a more preferable example, in the lithium composite oxide, the number of moles of Md2 to the total number of moles of M1 and M2, Md2/M, may be not lower than 0.0 and may be not higher than 0.2 or 0.1.
The lithium composite oxide includes a secondary particle, the secondary particle includes at least one primary particle, and the primary particle includes at least one crystallite.
As used herein, “at least one” refers to one or two or more.
As an example, the secondary particle may include one primary particle and may be formed by aggregation of two or more primary particles.
As an example, the primary particle may include one crystallite or may be formed by aggregation of two or more crystallites.
At least one selected from the secondary particle, the primary particle, and the crystallite includes a core and a shell occupying at least a part of the surface of the core.
As an example, the secondary particle may be a particle having a core-shell structure including a core and a shell occupying at least a part of the surface of the core.
In particular, the “at least a part” may mean being more than 0%, or not less than 10%, 20%, 30%, 40%, 50%, 60%, 70%, 80%, or 90% of the total surface area of the secondary particle.
The average diameter (D50) of the secondary particle may be 0.5 to 20 μm.
As an example, the thickness of the shell of the secondary particle may be more than 0 and not more than 10 μm, more than 0 and not more than 1 μm, more than 0 and not more than 500 nm, more than 0 and not more than 400 nm, more than 0 and not more than 300 nm, more than 0 and not more than 200 nm, more than 0 and not more than 150 nm, more than 0 and not more than 100 nm, more than 0 and not more than 90 nm, more than 0 and not more than 80 nm, more than 0 and not more than 70 nm, more than 0 and not more than 60 nm, or more than 0 and not more than 50 nm.
As an example, the thickness of the shell of the secondary particle may be more than 0.0% or not less than 1, 10, 20, 30, 40, 50, 60, 70, 80, or 90% and may be less than 100% or not more than 90, 80, 70, 60, 50, 40, 30, 20, 10, or 1%.
As an example, the primary particle may include a core and a shell occupying at least a part of the surface of the core.
In particular, the “at least a part” may mean being more than 0% or not less than 10%, 20%, 30%, 40%, 50%, 60%, 70%, 80%, or 90% of the total surface area of the primary particle.
As an example, the thickness of the shell of the primary particle may be more than 0 and not more than 10 μm, more than 0 and not more than 1 μm, more than 0 and not more than 500 nm, more than 0 and not more than 400 nm, more than 0 and not more than 300 nm, more than 0 and not more than 200 nm, more than 0 and not more than 150 nm, more than 0 and not more than 100 nm, more than 0 and not more than 90 nm, more than 0 and not more than 80 nm, more than 0 and not more than 70 nm, more than 0 and not more than 60 nm, or more than 0 and not more than 50 nm.
As an example, the thickness of the shell of the primary particle may be more than 0.0% or not less than 1, 10, 20, 30, 40, 50, 60, 70, 80, or 90% and may be less than 100% or not more than 90, 80, 70, 60, 50, 40, 30, 20, 10, or 1%.
As an example, the crystallite may include a core and a shell occupying at least a part of the surface of the core.
In particular, the “at least a part” may mean being more than 0% or not less than 10%, 20%, 30%, 40%, 50%, 60%, 70%, 80%, or 90% of the total surface area of the crystallite.
As an example, the thickness of the shell of the crystallite may be more than 0 and not more than 10 μm, more than 0 and not more than 1 μm, more than 0 and not more than 500 nm, more than 0 and not more than 400 nm, more than 0 and not more than 300 nm, more than 0 and not more than 200 nm, more than 0 and not more than 150 nm, more than 0 and not more than 100 nm, more than 0 and not more than 90 nm, more than 0 and not more than 80 nm, more than 0 and not more than 70 nm, more than 0 and not more than 60 nm, or more than 0 and not more than 50 nm.
As an example, the thickness of the shell of the crystallite may be more than 0.0% or not less than 1, 10, 20, 30, 40, 50, 60, 70, 80, or 90% and may be less than 100% or not more than 90, 80, 70, 60, 50, 40, 30, 20, 10, or 1%.
The “core” of the secondary particle, the primary particle, or the crystallite means a region that is present inside the secondary particle, the primary particle, or the crystallite and is close to the center of the particle excluding the surface of the particle. The “shell” means a region that is close to the surface excluding the center of the particle or the inside of the particle.
The “core” and “shell” of the secondary particle, the primary particle, or the crystallite of the present disclosure may be demarcated on the basis of a point where the pattern of the molar fraction or concentration change of an element included in the secondary particle, the primary particle, or the crystallite is distinguished. As an example, in the secondary particle, the primary particle, or the crystallite, the concentration of Ni rapidly decreases from the surface to the center in the shell, and then the gradient of the concentration is mitigated, maintained at a certain level, or increased in the core, so that the shell and the core are distinguished. As an example, in the secondary particle, the primary particle, or the crystallite, the concentration of Co rapidly decreases from the surface to the center in the shell, and then the gradient of the concentration is mitigated, maintained at a certain level, or increased in the core, so that the shell and the core are distinguished. As an example, in the secondary particle, the primary particle, or the crystallite, the concentration of Mn rapidly decreases from the surface to the center in the shell, and then the gradient of the concentration is mitigated, maintained at a certain level, or increased in the core, so that the shell and the core are distinguished.
In the cathode active material according to an embodiment of the present disclosure, a transition metal, such as nickel, cobalt, and/or manganese, may be diffused into the secondary particle, the primary particle, and/or the crystallite, to form the shell distinguishable from the core.
In the cathode active material according to an embodiment of the present disclosure, when the number of moles of at least one element selected from nickel (Ni), cobalt (Co), and manganese (Mn) to the total number of moles of M1 and M2 is NCM/M, the NCM/M in the shell is different than in the core of the secondary particle.
It may mean that on the cross-section across the inside of the secondary particle, the NCM/M in the shell is different than in the core of the secondary particle.
As an example, when the number of moles of nickel (Ni) to the total number of moles of M1 and M2 is Ni/M, the Ni/M in the shell may be different than in the core of the secondary particle.
As an example, when the number of moles of cobalt (Co) to the total number of moles of M1 and M2 is Co/M, the Co/M in the shell may be different than in the core of the secondary particle.
As an example, when the number of moles of manganese (Mn) to the total number of moles of M1 and M2 is Mn/M, the Mn/M in the shell may be different than in the core of the secondary particle.
As a more preferable example, the shell of the secondary particle may include a concentration gradient portion in which at least one element selected from nickel (Ni), cobalt (Co), and Manganese (Mn) has a concentration gradient.
This may mean that on the cross-section across the inside of the secondary particle, the shell of the secondary particle includes a concentration gradient portion in which at least one element selected from nickel (Ni), cobalt (Co), and manganese (Mn) has a concentration gradient.
In the cathode active material according to an embodiment of the present disclosure, the NCM/M in the shell may be different than in the core of the primary particle.
This may mean that on the cross-section across the inside of the primary particle, the NCM/M in the shell may be different than in the core of the primary particle.
As an example, the Ni/M in the shell may be different than in the core of the primary particle.
As an example, the Co/M in the shell may be different than in the core of the primary particle.
As an example, the Mn/M in the shell may be different than in the core of the primary particle.
In particular, the primary particle may be in contact with the surface of the secondary particle, and may include all of the primary particles present in the core of the secondary particle.
As a more preferable example, the shell of the primary particle may include a concentration gradient portion in which at least one element selected from nickel (Ni), cobalt (Co), and Manganese (Mn) has a concentration gradient.
This may mean that on the cross-section across the inside of the primary particle, the shell of the primary particle includes a concentration gradient portion in which at least one element selected from nickel (Ni), cobalt (Co), and manganese (Mn) has a concentration gradient.
In the cathode active material according to an embodiment of the present disclosure, the NCM/M in the shell may be different than in the core of the crystallite.
This may mean that on the cross-section across the inside of the crystallite, the NCM/M in the shell may be different than in the core of the crystallite.
As an example, the Ni/M in the shell may be different than in the core of the crystallite.
As an example, the Co/M in the shell may be different than in the core of the crystallite.
As an example, the Mn/M in the shell may be different than in the core of the crystallite.
As a more preferable example, the shell of the crystallite may include a concentration gradient portion in which at least one element selected from nickel (Ni), cobalt (Co), and Manganese (Mn) has a concentration gradient.
This may mean that on the cross-section across the inside of the crystallite, the shell of the crystallite includes a concentration gradient portion in which at least one element selected from nickel (Ni), cobalt (Co), and manganese (Mn) has a concentration gradient.
As a preferable example of the present disclosure, a concentration gradient portion of the transition metal may be formed in the shell of the crystallite as well as the secondary particle and the primary particle.
As a more preferable example, the Ni/M may be higher in the shell than in the core of at least one selected from the secondary particle, the primary particle, and the crystallite.
As a more preferable example, the shell of the secondary particle may include a concentration gradient portion in which the concentration of nickel (Ni) decreases toward the center from the surface of the secondary particle.
As a more preferable example, the shell of the primary particle may include a concentration gradient portion in which the concentration of nickel (Ni) decreases toward the center from the surface of the primary particle.
As a more preferable example, the shell of the crystallite may include a concentration gradient portion in which the concentration of nickel (Ni) decreases toward the center from the surface of the crystallite.
As a more preferable example, the Co/M may be higher in the shell than in the core of at least one selected from the secondary particle, the primary particle, and the crystallite.
As a more preferable example, the shell of the secondary particle may include a concentration gradient portion in which the concentration of cobalt (Co) decreases toward the center from the surface of the secondary particle.
As a more preferable example, the shell of the primary particle may include a concentration gradient portion in which the concentration of cobalt (Co) decreases toward the center from the surface of the primary particle.
As a more preferable example, the shell of the crystallite may include a concentration gradient portion in which the concentration of cobalt (Co) decreases toward the center from the surface of the crystallite.
As a still another preferable example, the cathode active material according to an embodiment of the present disclosure may not contain cobalt (Co).
In particular, the cathode active material includes a concentration gradient portion of nickel or manganese in the shell of the secondary particle, the primary particle, or the crystallite even without using expensive cobalt, and thus can suppress phase transition during life cycling of the cathode active material for a secondary battery, thereby increasing charge and discharge capacity and solving problems of life cycle deterioration and voltage decay.
As a more preferable example, in at least one selected from the secondary particle, the primary particle, and the crystallite, the Mn/M may be lower in the shell than in the core.
As a more preferable example, the shell of the secondary particle may include a concentration gradient portion in which the concentration of manganese (Mn) decreases toward the center from the surface of the secondary particle.
As a more preferable example, the shell of the primary particle may include a concentration gradient portion in which the concentration of manganese (Mn) increases toward the center from the surface of the primary particle.
As a more preferable example, the shell of the crystallite may include a concentration gradient portion in which the concentration of manganese (Mn) increases toward the center from the surface of the crystallite.
As a more preferable example of the present disclosure, the gradient in the concentration gradient portion of nickel (Ni) may be greater compared with that of manganese (Mn) or cobalt (Co) in the shell of the secondary particle, the primary particle, and/or the crystallite.
As a more preferable example of the present disclosure, the gradient in the concentration gradient portion of manganese (Mn) may be greater compared with that of nickel (Ni) or cobalt (Co) in the shell of the secondary particle, the primary particle, and/or the crystallite.
As a more preferable example of the present disclosure, the gradient in the concentration gradient portion of cobalt (Co) may be greater compared with that of nickel (Ni) or manganese (Mn) in the shell of the secondary particle, the primary particle, and/or the crystallite.
As a more preferable example of the present disclosure, the maximum Ni/M may be higher than in the minimum Mn/M in the shell of the secondary particle, the primary particle, and/or the crystallite.
As a more preferable example, the maximum Co/M may be lower than in the minimum Mn/M in the shell of the secondary particle, the primary particle, and/or the crystallite.
As a more preferable example, Mn/M>Ni/M>Co/M in the core of the secondary particle, the primary particle, and/or the crystallite.
As a more preferable example, the Ni/M may be not lower than 0.1, 0.2, or 0.3 and may be not higher than 1.0, 0.9, or 0.8 in the core of the secondary particle, the primary particle, and/or the crystallite.
As a more preferable example, the Co/M may be not higher than 0.3, 0.2, 0.1, or 0.05 and may be not lower than 0.0 in the core of the secondary particle, the primary particle, and/or the crystallite.
As a more preferable example, the Mn/M may be not lower than 0.4, 0.5, or 0.6 and may be not higher than 1.0, 0.9, or 0.8 in the core of the secondary particle, the primary particle, and/or the crystallite.
As a more preferable example of the present disclosure, the maximum Ni/M in the shell of the secondary particle, the primary particle, and/or the crystallite may be not less than 5, 10, 15, 20, 25, 30, 35, 40, 45, 50, 55, 60, 65, 70, 75, 80, 85, 90, or 95 mol % and may be not more than 100, 95, 90, 85, 80, 75, 70, 65, 60, 55, 50, 45, 40, 35, 30, 25, 20, 15, or 10 mol %.
As a still more preferable example of the present disclosure, the maximum Co/M in the shell of the secondary particle, the primary particle, and/or the crystallite may be not less than 1, 3, 5, 10, 15, 20, 25, 30, 35, 40, 45, 50, 55, 60, 65, 70, 75, 80, 85, 90, or 95 mol % and may be not more than 100, 95, 90, 85, 80, 75, 70, 65, 60, 55, 50, 45, 40, 35, 30, 25, 20, 15, or 10 mol %.
As a more preferable example of the present disclosure, the minimum Mn/M in the shell of the secondary particle, the primary particle, and/or the crystallite may be not less than 5, 10, 15, 20, 25, 30, 35, 40, 45, 50, 55, 60, 65, 70, 75, 80, 85, 90, or 95 mol % and may be not more than 100, 95, 90, 85, 80, 75, 70, 65, 60, 55, 50, 45, 40, 35, 30, 25, 20, 15, or 10 mol %.
As an example, the ratios of the R-3m space group and C2/m space group in the core and the shell of the secondary particle, the primary particle, and/or the crystallite may be different.
As an example, the ratios of Ni3+ and Ni2+ in the core and the shell of the secondary particle, the primary particle, and/or the crystallite may be different.
As an example, the ratios of Mn3+ and Mn4+ in the core and the shell of the secondary particle, the primary particle, and/or the crystallite may be different.
The cathode active material according to an embodiment of the present disclosure may further include a separate coating layer. The coating layer may contain at least one coating material selected from P, Nb, Si, Sn, Al, Pr, Al, Ti, Zr, Fe, Al, Fe, Co, Ca, Mn, Ti, Sm, Zr, Fe, La, Ce, Pr, Mg, Bi, Li, W, Co, Zr, B, Ba, F, K, Na, V, Ge, Ga, As, Sr, Y, Ta, Cr, Mo, W, Mn, Ir, Ni, Zn, In, Na, K, Rb, Cs, Fr, Sc, Cu, Ru, Rh, Pd, Ag, Cd, Sb, Hf, Ta, Re, Os, Pt, Au, Pb, Bi, and Po, but is not particularly limited thereto.
The coating layer blocks the contact between the cathode active material and an electrolyte included in the lithium secondary battery to suppress the occurrence of side reactions, thereby improving the life cycle and increasing packing density. In some embodiments, the coating layer can act as a lithium ion conductor.
The coating layer may be formed on the entire surface of the cathode active material or the entire surface of the primary particle, or may be partially formed thereon. In addition, the coating layer may be in a single-layer coating, double-layer coating, grain boundary coating, uniform coating, or island coating form.
In the cathode active material according to an embodiment of the present disclosure, a lithium ion diffusion path may be formed inside the primary particle.
In the cathode active material according to an embodiment, a surface that constitutes a layer of the layered structure may have crystal orientation in a direction perpendicular to a C-axis inside the primary particle, and the lithium ion diffusion path may be formed inside or outside the primary particle in a direction toward the center of the particle of the cathode active material.
Hereinafter, a method for preparing a cathode active material for a secondary battery according to an embodiment of the present disclosure will be described in detail.
First, a step of forming precursor particles is performed.
As a more preferable example, the precursor particles may be manufactured by co-precipitation, and a complexing agent may be added for the manufacturing.
Then, a step of subjecting the formed precursor particles to first thermal treatment at 300 to 1000° C. followed by cooling is performed.
Then, a step of, after the first thermal treatment and then cooling, subjecting the precursor particles to wet coating with a compound containing at least one element selected from cobalt, nickel, and manganese may be performed.
Then, a step of mixing a first lithium compound with the first thermally treated and then cooled particles or the wet-coated particles and subjecting the mixture to second thermal treatment at 800 to 1000° C., followed by cooling is performed.
Then, a step of, after the second thermal treatment and then cooling, subjecting the precursor particles to wet coating with a compound containing at least one element selected from cobalt, nickel, and manganese may be performed.
Then, a step of mixing a second lithium compound with the second thermally treated and then cooled particles or the wet-coated particles and subjecting the mixture to third thermal treatment at 300 to 1000° C., followed by cooling is performed.
An embodiment of the present disclosure may include a step of subjecting the precursor particles to wet coating with a compound containing at least one element selected from cobalt, nickel, and manganese, after the step of forming the precursor particles before the step of first thermal treatment followed by cooling, between the step of first thermal treatment followed by cooling and the step of second thermal treatment followed by cooling, and between the step of second thermal treatment followed by cooling and the step of third thermal treatment followed by cooling.
As a more preferable example, in the step of wet coating, co-precipitation may be performed, and a complexing agent may be added.
A secondary battery according to an embodiment of the present disclosure includes the cathode active material.
The cathode active material is as described above, and a binder, a conductor, and a solvent are not particularly limited as long as these can be used on a cathode current collector for a secondary battery.
The lithium secondary battery may specifically include a cathode, an anode disposed to face the cathode, and an electrolyte between the cathode and the anode, and any battery that can be used as a secondary battery is not particularly limited thereto.
Hereinafter, cathode active materials according to examples of the present disclosure are specifically described.
Preparation of Precursor
A spherical NixCoyMnz(OH) precursor was synthesized using co-precipitation. In a 90-L reactor, 25 wt % of NaOH and 28 wt % of NH4OH were added to an aqueous solution of 2.5 M complex transition-metal sulfates prepared by mixing NiSO4·6H2O, MnSO4·H2O, and CoSO4·7H2O while the mole ratio of Ni:Co:Mn was adjusted. The pH in the reactor was maintained at 9.0-12.0, and the temperature in the reactor was maintained at 45 to 50° C. In addition, N2, an inert gas, was injected into the reactor to prevent the oxidation of the prepared precursor. After the completion of synthesis and stirring, washing and dehydration were performed using a filter press (F/P). Finally, the dehydrated product was dried at 120° C. for 2 days, and filtered through a 75-μm (200 mesh) sieve to obtain a NixCoyMnz(OH) precursor of 4 μm.
First Thermal Treatment and Cooling
The precursor was maintained in an O2 or air (50 L/min) atmosphere in a box furnace while the temperature was elevated at a rate of 2° C. per min and maintained at 300 to 1000° C. for 1-10 hours, followed by furnace cooling.
Wet Coating (if Performed after the First Thermal Treatment and Cooling)
The precursor was wet-coated using co-precipitation. In a reactor in which the precursor was stirred, an aqueous solution of complex transition-metal sulfates, which was prepared by mixing CoSO4·7H2O, NiSO4·6H2O, or MnSO4·H2O with an adjusted molar ratio and distilled water, 25 wt % of NaOH, and 28 wt % of NH4OH were added. The coating amount of the transition metal was 1-10 mol % relative to the total number of moles of nickel (Ni), cobalt (Co), and manganese (Mn), and the pH in the reactor was maintained at 9.0-12.0. After the completion of synthesis and stirring, washing and dehydration were performed using a filter press (F/P). Finally, the dehydrated product was dried at 150° C. for 14 hours to obtain a precursor having a concentration gradient.
Second Thermal Treatment and Cooling
The precursor was mixed with LiOH or Li2CO3, which was weighed with an adjusted Li/M ratio, by using a manual mixer (MM). The mixture was maintained in an O2 or air (50 L/min) atmosphere in a Box furnace while the temperature was elevated at a rate of 2° C. per min and maintained at 800 to 1000° C. for 7-12 hours, followed by furnace cooling.
Wet Coating (if Performed after the Second Thermal Treatment and Cooling)
The lithium composite oxide was wet-coated using co-precipitation. In a reactor in which the particles were stirred, an aqueous solution of complex transition-metal sulfates, which was prepared by mixing CoSO4·7H2O, NiSO4·6H2O, or MnSO4·H2O with an adjusted molar ratio and distilled water, 25 wt % of NaOH, and 28 wt % of NH4OH were added. The coating amount of the transition metal was 1-10 mol % relative to the total number of moles of nickel (Ni), cobalt (Co), and manganese (Mn), and the pH in the reactor was maintained at 9.0-12.0. After the completion of synthesis and stirring, washing and dehydration were performed using a filter press (F/P). Finally, the dehydrated product was dried at 150° C. for 14 hours to obtain a lithium composite oxide having a concentration gradient.
Third Thermal Treatment and Cooling
The coated product was mixed with LiOH or Li2CO3, which was weighed with an adjusted Li/M ratio, by using a manual mixer (MM). The mixture was maintained in an O2 or air atmosphere in a box furnace while the temperature was elevated at a rate of 4.4° C. per min and maintained at 300 to 1000° C. for 7-12 hours, followed by furnace cooling.
Each cathode active material was prepared by the same method as in Examples 1 to 5 except that a step of wet coating with a transition metal as in the manufacturing of Examples 1 to 5 was not performed.
Table 1 below relates to the manufacturing methods of Examples 1 to 5 and Comparative Examples 1 to 2.
indicates data missing or illegible when filed
Cathode slurries were prepared by dispersion of 90 wt % of the cathode active materials of the examples and comparative examples, 5.5 wt % of carbon black, and 4.5 wt % of a PVDF binder in 30 g of N-methyl-2 pyrrolidone (NMP). Each of the cathode slurries was applied to a 15 μm-thick aluminum (Al) thin film as a cathode current collector, dried, and then roll-pressed to manufacture a cathode.
For the cathode, metallic lithium was used as a counter electrode, and 1.15 M LiPF6 in EC/DMC/EMC=2/4/4 (vol %) was used as an electrolyte.
A separator formed of a porous polyethylene (PE) film was interposed between the cathode and the anode to form a battery assembly, and the electrolyte was injected into the battery assembly to manufacture a lithium secondary battery (coin cell)
Table 2 below relates to characteristics of lithium secondary batteries of the examples and comparative examples.
indicates data missing or illegible when filed
The FQ-EDS analysis results of
It can also be confirmed that even the cathode active material of Example 5 containing no cobalt and employing wet coating with nickel (Ni) had a similar concentration gradient to the cathode active materials employing wet coating with cobalt (Co).
The TEM-EDS analysis results of
The TEM-EDS analysis results of
Referring to
Referring to
Referring to
Referring to
Referring to
| Number | Date | Country | Kind |
|---|---|---|---|
| 10-2020-0168858 | Dec 2020 | KR | national |
| 10-2021-0067237 | May 2021 | KR | national |
| 10-2021-0080132 | Jun 2021 | KR | national |
| 10-2021-0080133 | Jun 2021 | KR | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/KR2021/018083 | 12/2/2021 | WO |
