Patent Application
20200343551
This application claims priority to and the benefit of Korean Patent Application No. 10-2019-0058373 filed in the Korean Intellectual Property Office on May 17, 2019, Korean Patent Application No. 10-2019-0049393 filed in the Korean Intellectual Property Office on Apr. 26, 2019, and Korean Patent Application No. 10-2020-0039301 filed in the Korean Intellectual Property Office on Mar. 31, 2020, the entire content of each of which is incorporated herein by reference.
One or more embodiments of the present invention relate to a positive active material for a rechargeable lithium battery, a method of preparing the same, and a rechargeable lithium battery including the same.
Rechargeable lithium batteries are used in a variety of applications because they have a high voltage and a high energy density. For example, electric vehicles utilize lithium rechargeable batteries having improved discharge capacity and life-span characteristics because they can operate at high temperatures, should charge and/or discharge large amounts of electricity, and should be used for a long time.
As a positive active material for lithium rechargeable batteries, a nickel-based lithium metal oxide has been widely used as a positive active material due to improved capacity characteristics. However, the nickel-based lithium metal oxide may exhibit deteriorated cell characteristics due to a side-reaction with an electrolyte solution, and thus improvement therefore is desirable.
An embodiment of the present disclosure provides a positive active material that easily intercalates/deintercalates lithium ions and provides improved power output characteristics.
Another embodiment provides a method of preparing the positive active material.
Another embodiment provides a rechargeable lithium battery having improved power output characteristics by employing a positive electrode including the positive active material.
An embodiment provides a positive active material for a rechargeable lithium battery including a nickel-based lithium metal oxide having a layered crystal structure and a coating layer including a lithium-metal oxide selectively disposed on (003) crystalline plane of the nickel-based lithium metal oxide, wherein the nickel-based lithium metal oxide exists as single particles.
The single particles may have a particle diameter of about 200 nm to about 6 μm, for example about 3 μm to about 6 μm.
The lithium-metal oxide may have a monoclinic crystal system having a C2/c space group crystal structure.
A lattice mismatch ratio between a (003) crystalline plane of the nickel-based lithium metal oxide and a (00I) crystalline plane (wherein I is 1, 2, or 3) of the lithium-metal oxide may be less than or equal to about 15%.
The lithium-metal oxide may include a compound represented by Chemical Formula 1, a compound represented by Chemical Formula 2, or a combination thereof.
Li2MO3 Chemical Formula 1
Li8MO6. Chemical Formula 2
In Chemical Formula 1 and Chemical Formula 2,
M is a metal having an oxidation number of 4.
The lithium-metal oxide may include Li2SnO3, Li2ZrO, Li2TeO3, Li2RuO3, Li2TiO3, Li2MnO3, Li2PbO3, Li2HfO3, Li8SnO6, Li8ZrO6, Li8TeO6, Li8RuO6, Li8TiO6, Li8MnO6, Li8PbO6, Li8Hf6, or a combination thereof.
A content of the lithium-metal oxide may be about 0.1 mol % to about 5 mol % based on a total amount of the nickel-based lithium metal oxide and the lithium-metal oxide.
The coating layer may have a thickness of about 1 nm to about 100 nm.
The nickel-based lithium metal oxide and the lithium-metal oxide selectively disposed on the (003) crystalline plane of the nickel-based lithium metal oxide may each have a layered structure that is epitaxially grown in a same c-axis direction.
The nickel-based lithium metal oxide may include a compound represented by Chemical Formula 3, a compound represented by Chemical Formula 4, or a combination thereof.
LiaNixCoyQ11-x-yO2. Chemical Formula 3
In Chemical Formula 3,
0.9≤a≤1.05, 0.6≤x≤0.98, 0.01≤y≤0.40, and Q1 is at least one metal element selected from Mn, Al, Cr, Fe, V, Mg, Nb, Mo, W, Cu, Zn, Ga, In, La, Ce, Sn, Zr, Te, Ru, Ti, Pb, and Hf.
LiaNixQ21-xO2. Chemical Formula 4
In Chemical Formula 4,
0.9≤a≤1.05, 0.6≤x≤1.0, and Q2 is at least one metal element selected from Mn, Al, Cr, Fe, V, Mg, Nb, Mo, W, Cu, Zn, Ga, In, La, Ce, Sn, Zr, Te, Ru, Ti, Pb, and Hf.
Another embodiment provides a method of preparing a positive active material for a rechargeable lithium battery that includes mixing a first precursor for forming lithium-metal (M) oxide, a second precursor for forming nickel-based lithium metal oxide, and a lithium precursor to obtain a mixture in a solid-phase powder, and heat-treating the mixture.
The heat-treating may be performed at a temperature in a range of about 600° C. to about 950° C. at a temperature-increasing rate of about 5° C./min.
The method may further include cooling the heat-treated resultant at a cooling rate of less than or equal to about 1° C./min.
The first precursor may include a metal (M)-containing oxide, a metal (M)-containing halide, a metal (M)-containing sulfate, a metal (M)-containing hydroxide, a metal (M)-containing nitrate, a metal (M)-containing carboxylate, a metal (M)-containing oxalate, or a combination thereof.
Another embodiment provides a method of preparing a positive active material for a rechargeable lithium battery that includes:
mixing a first precursor for forming lithium-metal (M) oxide, a second precursor for forming nickel-based lithium metal oxide, and a lithium precursor with a solvent to obtain a precursor composition,
adding a chelating agent to the precursor composition and mixing to form a gel,
first heat-treating the gel to obtain a first product, and
second heat-treating the first product to obtain a second product.
The first heat-treating may be performed at a temperature in a range of about 250° C. to about 400° C.
The second heat-treating may be performed at a temperature in a range of about 700° C. to about 950° C. at a temperature-increasing rate of less than or equal to about 5° C./min.
The method may further include cooling the heat-treated resultant at a cooling rate of less than or equal to about 1° C./min.
The first precursor may include a metal (M)-containing halide, a metal (M)-containing sulfate, a metal (M)-containing hydroxide, a metal (M)-containing nitrate, a metal (M)-containing carboxylate, a metal (M)-containing oxalate, or a combination thereof.
The second precursor may include at least one nickel precursor selected from Ni(OH)2, NiO, NiOOH, NiCO3.2Ni(OH)2.4H2O, NiC2O4.2H2O, Ni(NO3)2.6H2O, NiSO4, NiSO4.6H2O, a nickel fatty acid salt, and a nickel halide.
The lithium precursor may include a lithium hydroxide, a lithium nitrate, a lithium carbonate, a lithium acetate, a lithium sulfate, a lithium chloride, a lithium fluoride, or a mixture thereof.
Another embodiment provides a rechargeable lithium battery including the positive active material.
The positive active material includes a coating layer formed only on (substantially parallel only to) the (003) crystalline plane in a c-axis direction, so that the charge transfer resistance does not increase, compared with the positive active material including a coating layer formed on the crystalline plane in a-axis and b-axis directions, resulting in providing a rechargeable lithium battery having improved power output characteristics.
In addition, the positive active material has high voltage characteristics, and by adopting such a positive active material, a positive electrode for a rechargeable lithium battery having improved positive electrode slurry stability and active mass density of an electrode during electrode manufacturing process may be fabricated. By adopting the positive active material, it is possible to fabricate a rechargeable lithium battery that exhibits reduced gas generation at a high voltage, and improved reliability and safety.
The accompanying drawings, together with the specification, illustrate embodiments of the subject matter of the present disclosure, and, together with the description, serve to explain principles of embodiments of the subject matter of the present disclosure.
Hereinafter, further detailed descriptions will be given of a rechargeable lithium battery including a positive active material for a rechargeable lithium battery according to an embodiment, of a positive electrode including the positive active material, and of a manufacturing method thereof. However, these are example embodiments, the present disclosure is not limited thereto and the subject matter of the present disclosure is defined by the scope of the appended claims, and equivalents thereof.
As used herein, the term “particle diameter” refers to average particle diameter (D50) which is a median value in a particle size distribution, as determined using a particle size analyzer. In some embodiments, the “particle diameter” refers to the average value of the longest length or dimension of the particle which is not spherical particle.
A positive active material for a rechargeable lithium battery according to an embodiment includes a nickel-based lithium metal oxide having a layered crystal structure and a coating layer including a lithium-metal oxide selectively disposed on (003) crystalline plane of the nickel-based lithium metal oxide, wherein the nickel-based lithium metal oxide exists as single particles.
In order to improve electrochemical characteristics of the nickel-based lithium metal oxide, a method of coating a metal oxide-based or phosphate-based material on the surface thereof has been performed. However, when this method is performed, the metal oxide-based or phosphate-based material is non-selectively coated on the whole surface of the nickel-based lithium metal oxide. As a result, charge transfer resistance of the metal oxide-based or phosphate-based material may be increased and thus power output characteristics of a rechargeable lithium battery including a positive electrode using the same may be deteriorated.
In order to solve the aforementioned problem, the positive active material according to embodiments of the present disclosure may effectively (or suitably) suppress (or reduce) the charge transfer resistance increase without generally (or substantially) interfering with lithium intercalation and deintercalation due to the surface coating of the nickel-based lithium metal oxide by forming a coating layer selectively, e.g., by including a lithium-metal oxide not on a crystalline plane where lithium ions are intercalated/deintercalated, but on the other (003) crystalline plane of the nickel-based lithium metal oxide.
In the positive active material of the present embodiments, the coating layer including the lithium-metal oxide is selectively disposed on a plane where lithium ions are not intercalated and deintercalated, that is, the (003) crystalline plane of the nickel-based lithium metal oxide.
The single particles of the nickel-based lithium metal oxide may have a particle diameter of, for example, greater than or equal to about 200 nm, greater than or equal to about 300 nm, greater than or equal to about 400 nm, greater than or equal to about 500 nm, greater than or equal to about 600 nm, greater than or equal to about 700 nm, greater than or equal to about 800 nm, greater than or equal to about 900 nm, greater than or equal to about 1 μm, greater than or equal to about 1.5 μm, greater than or equal to about 2 μm, greater than or equal to about 2.5 μm, or greater than or equal to about 3.0 μm and less than or equal to about 6 μm, less than or equal to about 5.5 μm, less than or equal to about 5 μm, less than or equal to about 4.7 μm, less than or equal to about 4.5 μm, less than or equal to about 4.3 μm, less than or equal to about 4.0 μm, or less than or equal to about 3.5 μm. When the particle diameter of the single particles is within any of these ranges, gas generation at high voltage may be reduced when a lithium rechargeable battery is manufactured using the same, and reliability and safety of the lithium rechargeable battery may be secured.
The lithium-metal oxide may have a C2/c space group crystal structure of a monoclinic crystal system. When the lithium-metal oxide has this crystal structure, a lattice mismatch on the interface thereof with the nickel-based lithium metal oxide may be minimized.
For example, the lattice mismatch of the (003) crystalline plane of the nickel-based lithium metal oxide and a (00I) crystalline plane (I is 1, 2, or 3) of the lithium-metal oxide may have a ratio of less than or equal to about 15%, for example, less than or equal to about 13%, less than or equal to about 12%, less than or equal to about 11%, less than or equal to about 10%, less than or equal to about 9%, less than or equal to about 8%, less than or equal to about 7%, less than or equal to about 6%, less than or equal to about 5%, less than or equal to about 4%, or less than or equal to about 3%. When the lattice mismatch has the ratio within the range described herein, the (003) crystalline plane of a Li—O octahedron structure of the nickel-based lithium metal oxide and the (00I) crystalline plane (I is 1, 2, or 3) of a Li—O octahedron structure of the lithium-metal oxide may be well shared with each other, and the coating layer including the lithium-metal oxide may not be separated on the interface, but may be stably (or suitably) present.
The lattice mismatch ratio (%) may be calculated by Equation 1.
|A-B|/B×100. Equation 1
In Equation 1, A indicates an oxygen-oxygen bond length of the (003) crystalline plane of the nickel-based lithium metal oxide, and B indicates an oxygen-oxygen bond length of the (00I) crystalline plane (I is 1, 2, or 3) of the lithium-metal oxide.
In an embodiment, when the nickel-based lithium metal oxide is LiNiO2, and the lithium-metal (M) oxide is Li2MO3 of Chemical Formula 1 or Li8MO6 of Chemical Formula 2, the lattice mismatch ratio is the same as shown in Table 1. The oxygen-oxygen bond length of the (003) crystalline plane of LiNiO2 is about 2.875 Å.
Table 1 shows that the lithium-metal oxides such as Li2MO3 and LiMO6 have a lattice mismatch ratio of less than or equal to 15%, indicating that these lithium-metal oxides may be coated on the (003) crystalline plane of the layered nickel-based lithium metal oxide of LiNiO2.
The lithium-metal oxide may include a compound represented by Chemical Formula 1, a compound represented by Chemical Formula 2, or a combination thereof.
Li2MO3 Chemical Formula 1
Li8MO6 Chemical Formula 2
In Chemical Formulae 1 and 2, M is a metal having an oxidation number of 4.
The lithium-metal oxide may include Li2SnO3, Li2ZrO3, Li2TeO3, Li2RuO3, Li2TiO3, Li2MnO3, Li2PbO3, Li2HfO3, Li8SnO6, Li8ZrO6, Li8TeO6, Li8RuO6, Li8TiO6, Li8MnO6, Li8PbO6, Li8Hf6, and/or a combination thereof.
An amount of the lithium-metal oxide may be less than or equal to about 5 mol %, for example greater than or equal to about 0.1 mol %, greater than or equal to about 0.2 mol %, greater than or equal to about 0.5 mol %, greater than or equal to about 1 mol %, greater than or equal to about 1.5 mol %, or greater than or equal to about 2 mol % and less than or equal to about 5 mol %, less than or equal to about 4.5 mol %, less than or equal to about 4 mol %, or less than or equal to about 3 mol % based on a total amount of the nickel-based lithium metal oxide and the lithium-metal oxide. When the amount of the lithium-metal oxide is within the range described herein, the coating layer on the (003) crystalline plane of the nickel-based lithium metal oxide may effectively (or suitably) suppress (or reduce) an increase of the charge transfer resistance.
The positive active material according to an embodiment has a structure that the coating layer including the lithium-metal oxide is stacked on one plane of the nickel-based lithium metal oxide. The coating layer may be selectively disposed on the (003) crystalline plane of the nickel-based lithium metal oxide.
The coating layer may have a thickness of greater than or equal to about 1 nm, for example, greater than or equal to about 5 nm, greater than or equal to about 10 nm, greater than or equal to about 20 nm, greater than or equal to about 30 nm, greater than or equal to about 40 nm, greater than or equal to about 50 nm, greater than or equal to about 60 nm, greater than or equal to about 70 nm, greater than or equal to about 80 nm, or greater than or equal to about 90 nm and less than or equal to about 100 nm, less than or equal to about 90 nm, less than or equal to about 80 nm, less than or equal to about 70 nm, less than or equal to about 60 nm, less than or equal to about 50 nm, less than or equal to about 40 nm, less than or equal to about 30 nm, less than or equal to about 20 nm, or less than or equal to about 10 nm. When the coating layer has a thickness within any of these ranges, the charge transfer resistance of the nickel-based lithium metal oxide may be effectively (or suitably) blocked (or protected) from being increased due to the coating.
The coating layer may be a continuous or discontinuous film.
In the positive active material according to an embodiment, the lithium-metal oxide selectively disposed on the (003) crystalline plane of the nickel-based lithium metal oxide and the nickel-based lithium metal oxide may each have an epitaxially grown layered structure in a same c-axis direction. As used herein, the terms “c-axis direction,” “a-axis direction,” and “b-axis direction” may each independently refer to a direction along an axis of symmetry of the respective space group, where the c-axis is the major axis of symmetry. For example, the c-axis direction may refer to the direction along the C2 axis of the C2/c space group of the lithium-metal oxide and/or the major axis of symmetry of the space group of the nickel-based lithium metal oxide (e.g., the R3m space group). The c-axis direction of the lithium-metal oxide and the nickel-based lithium metal oxide may be the same or substantially the same. Here, the epitaxially grown layered structure in the c-axis direction may be confirmed by using a TEM (transmission electron microscope) image and an FFT (fast fourier transformation) pattern of the TEM image.
The nickel-based lithium metal oxide coated with the coating layer of the present embodiments may have a layered crystal structure. The nickel-based lithium metal oxide having such a layered crystal structure may include a compound represented by Chemical Formula 3, a compound represented by Chemical Formula 4, or a combination thereof.
LiaNixCoyQ11-x-yO2. Chemical Formula 3
In Chemical Formula 3,
0.9≤a≤1.05, 0.6≤x≤0.98, 0.01≤y≤0.40, and Q1 is at least one metal element selected from Mn, Al, Cr, Fe, V, Mg, Nb, Mo, W, Cu, Zn, Ga, In, La, Ce, Sn, Zr, Te, Ru, Ti, Pb, and Hf.
LiaNixQ21-xO2. Chemical Formula 4
In Chemical Formula 4,
0.9≤a≤1.05, 0.6≤x≤1.0, and Q2 is at least one metal element selected from Mn, Al, Cr, Fe, V, Mg, Nb, Mo, W, Cu, Zn, Ga, In, La, Ce, Sn, Zr, Te, Ru, Ti, Pb, and Hf.
The nickel-based lithium metal oxide may be a nickel-based lithium transition metal oxide when the compound includes a transition metal.
In an embodiment, the nickel-based lithium metal oxide may further include at least one element selected from calcium (Ca), strontium (Sr), boron (B), and fluorine (F). If the positive electrode is fabricated using the nickel-based lithium metal oxide that further includes these elements, electrochemical characteristics of the rechargeable lithium battery may be further improved. A content of the element(s) may be about 0.001 mol to about 0.1 mol relative to 1 mol of the metal.
The nickel-based lithium metal oxide may have a layered structure such as that of α-NaFeO2, in which NixCoyQ11-x-yO2 or NixQ21-xO2 and a Li layer are successively intersected, and may have an R-3m space group (e.g., the R3m space group). The space groups described herein have the same meaning as commonly understood in the art to which this disclosure pertains, and may be referred to utilizing, e.g., the short name (e.g., the international short symbol).
In an embodiment, a (003) peak may have a full width at half maximum in a range of about 0.120° to about 0.125° in an X-ray diffraction spectrum analysis of the nickel-based lithium metal oxide. In addition, the positive active material may have a (104) peak showing a full width at half maximum of about 0.105° to about 0.110° and a (110) peak showing a full width at half maximum of about 0.110° to about 0.120°. These full widths at half maximum exhibit (reflect) crystallinity of the nickel-based lithium metal oxide.
In one or more embodiments, the nickel-based lithium metal oxide exhibits a full width at half maximum of the (003) peak within a range of about 0.130° to about 0.150° in the X-ray diffraction analysis spectrum. The lower the full width at half maximum is, the higher the crystallinity of the nickel-based lithium metal oxide is. Accordingly, the nickel-based lithium metal oxide according to an embodiment of the present invention exhibits high crystallinity compared with a comparable nickel-based lithium metal oxide in the related art. When the nickel-based lithium metal oxide having higher crystallinity is used as a positive active material, a rechargeable lithium battery securing safety at a high voltage may be manufactured.
In the nickel-based lithium metal oxide, a percentage (cation mixing ratio) of nickel ions occupying a lithium site may be less than or equal to about 2.0 atom %, for example, about 0.0001 atom % to about 1.5 atom %. In a high-temperature firing process, Ni ions (Ni2+) having a similar ion radius (e.g., having an ion radius of about 0.83 Å) to that of lithium ions (Li+) (e.g., having an ion radius of about 0.90 Å) are mingled into a lithium ion-diffusing surface, and thus tend to be more possibly prepared into a nonstoichiometric composition of [Li1-xNix]3b[Ni]3a[O2]6c (wherein a, b, and c indicate site positions of a structure, and x indicates the number of the Ni ions moving toward the Li site, 0≤x<1). Accordingly, when Ni2+ is mixed into the lithium site, the site may be a locally irregularly-aligned rock-salt layer (Fm3m) and thus is not only electrochemically inactive but also hinders the lithium ions of a lithium layer from solid-phase diffusion and thus suppresses (or reduces) a battery reaction. The nickel-based lithium metal oxide may have improved battery characteristics by suppressing (or reducing) such cation mixing ratio.
The crystal structure of the positive active material may include a hexagonal crystal structure according to the XRD analysis, and an a-axis may have a length of about 2.867 Å to about 2.889 Å, a c-axis may have a length of about 14.228 Å to about 14.270 Å, and accordingly, a unit lattice (unit cell) volume may be in a range of about 101.35 Å3 to about 102.98 Å3.
The XRD analysis may be performed by using a CuK-alpha ray (X-ray wavelength: about 1.541 Å) as a light source.
The positive active material according to an embodiment may suppress (or reduce) a surface side-reaction of residual lithium with an electrolyte solution by adjusting a mixing weight ratio of lithium relative to a metal and controlling heat-treatment conditions (a heat-treatment temperature, atmosphere, and/or time) during the preparation process of the positive active material, to adjust sizes of the single particles of the positive active material, thus reducing a specific surface area of the positive active material and substantially removing the residual lithium. As described above, when the manufacturing process may be controlled, crystallinity of the positive active material may be improved, and stability thereof may be secured.
In the positive active material, a content of the residual lithium may be less than or equal to about 0.1 wt %. For example, a content of LiOH may be in a range of about 0.01 wt % to about 0.06 wt %, and a content Li2CO3 may be in a range of about 0.05 wt % to about 0.1 wt %. Herein, the contents (e.g., amounts) of LiOH and Li2CO3 may be measured utilizing a titration method.
In the positive active material, a content (e.g., amount) of the lithium carbonate (Li2CO3), measured through a GC-MS analysis, may be in a range of about 0.01 wt % to about 0.05 wt %. As described above, when the content of the residual lithium is small, a side-reaction of the residual lithium with an electrolyte solution may be suppressed (or reduced), and gas generation at a high voltage and a high temperature may be suppressed (or reduced), and accordingly, the positive active material may exhibit excellent safety. In addition, when the content of LiOH is small, pH of the positive electrode slurry is decreased during the manufacturing process, and accordingly, the positive electrode slurry may be stable and thus accomplish uniform (or substantially uniform) electrode plate coating. This LiOH decrease may secure slurry stability during the slurry manufacturing process for the positive electrode coating.
The positive active material may exhibit characteristics of a high onset point temperature of about 250° C. to about 270° C. compared with that of a comparable commercially-available nickel-based lithium metal oxide (e.g., NCM) in a differential scanning calorimetry analysis and a decreased instantaneous heat release rate of a main peak. When the positive active material exhibits these characteristics, high temperature safety of a lithium ion rechargeable battery may be realized.
Because the positive active material according to the present embodiments may suppress (or reduce) the side-reaction of the nickel-based lithium metal oxide with an electrolyte solution, thermal stability and structural stability of the nickel-based lithium metal oxide are improved, and thus stability and charge and discharge characteristics of a rechargeable lithium battery including the positive active material may be improved.
Hereinafter, a method of preparing the positive active material according to an embodiment is described.
A method of preparing a positive active material for a rechargeable lithium battery according to an embodiment includes mixing a first precursor for forming lithium-metal (M) oxide, a second precursor for forming nickel-based lithium metal oxide, and a lithium precursor to obtain a mixture in a solid-phase powder, and heat-treating the mixture.
First, the first precursor for forming the lithium-metal (M) oxide, the second precursor for forming the nickel-based lithium metal oxide, and the lithium precursor are mixed in a solid-phase powder without a solvent to obtain a mixture. The contents of the first precursor for forming the lithium-metal (M) oxide, the second precursor for forming the nickel-based lithium metal oxide and lithium precursor may be properly adjusted to obtain the positive active material having a desired composition.
For example, when the first precursor for forming the lithium-metal (M) oxide is included in an amount of x mole (0<x≤0.1, 0<x≤0.09, 0<x≤0.08, 0<x≤0.07, 0<x≤0.06, 0<x≤0.05, 0<x≤0.04, 0<x≤0.03, 0<x≤0.02, 0<x≤0.01, 0.01<x≤0.05, 0.02<x≤0.05, or 0.02<x≤0.03), an amount of the second precursor for forming the nickel-based lithium metal oxide is (1-x) mole, and an amount of the lithium precursor may be adjusted to have a mixing ratio of about 1.03(1+x) mole.
The precursors are ball-milled at about 400 rpm to about 600 rpm for about 2 hours to about 5 hours to obtain a uniform mixture.
Subsequently, the uniform mixture is heat-treated to obtain a positive active material for a lithium rechargeable battery.
The heat treatment may be performed for example, at a temperature in a range of greater than or equal to about 600° C., greater than or equal to about 610° C., greater than or equal to about 620, greater than or equal to about 630° C., greater than or equal to about 640° C., greater than or equal to about 650° C., greater than or equal to about 660° C., greater than or equal to about 670° C., greater than or equal to about 680° C., greater than or equal to about 690° C., greater than or equal to about 700° C., greater than or equal to about 710° C., greater than or equal to about 720° C., greater than or equal to about 730° C., greater than or equal to about 740° C., or greater than or equal to about 750° C. and for example less than or equal to about 950° C., less than or equal to about 940° C., less than or equal to about 930° C., less than or equal to about 920° C., less than or equal to about 910° C., less than or equal to about 900° C., less than or equal to about 890° C., less than or equal to about 880° C., less than or equal to about 870° C., less than or equal to about 860° C., less than or equal to about 850° C., less than or equal to about 840° C., less than or equal to about 830° C., less than or equal to about 820° C., less than or equal to about 810° C., or less than or equal to about 800° C. Herein, the heat treatment may include firing the mixed solid powders within any of these temperature ranges for about 5 hours to about 15 hours under a high pressure. In addition, a temperature-increasing rate of the heat treatment may be each independently less than or equal to about 5° C./min, for example, less than or equal to about 4° C./min, for example, less than or equal to about 3° C./min, for example, less than or equal to about 2° C./min, or for example, less than or equal to about 1° C./min.
The cooling rate ensuing the second heat-treating may be for example, less than or equal to about 1° C./min, for example, less than or equal to about 0.7° C./min, for example, less than or equal to about 0.5° C./min, for example, less than or equal to about 0.3° C./min, or for example, less than or equal to about 0.1° C./min.
When the heat-treating is performed within any of these ranges, phase-separation of the lithium-metal oxide may easily occur, and the coating layer including the lithium-metal oxide may be stably formed on the (003) crystalline plane of the nickel-based lithium metal oxide.
In the method, the first precursor for forming lithium-metal (M) oxide may include a metal (M)-containing oxide, a metal (M)-containing halide, a metal (M)-containing sulfate, a metal (M)-containing hydroxide, a metal (M)-containing nitrate, a metal (M)-containing carboxylate, a metal (M)-containing oxalate, or a combination thereof. Non-limiting examples of the first precursor may include tin oxide (SnO2), zirconium chloride (ZrCl4), tellurium oxide (TeO2), ruthenium oxide (RuO2), titanium oxide (TiO2), manganese oxide (MnO2), hafnium oxide (HfO2), lead oxide (PbO2), tin chloride (SnCl2), tellurium chloride (TeCl4), ruthenium chloride (RuCl4), titanium chloride (TiCl4), manganese chloride (MnCl4), hafnium chloride (HfCl4), lead chloride (PbCl4), tin sulfate (SnSO4), zirconium sulfate (Zr(SO4)2), tellurium sulfate (Te(SO4)2), ruthenium sulfate (Ru(SO4)2), titanium sulfate (Ti(SO4)2), manganese sulfate (Mn(SO4)2), hafnium sulfate (Hf(SO4)2), lead sulfate (Pb(SO4)2), tin hydroxide, zirconium hydroxide, tellurium hydroxide, ruthenium hydroxide, titanium hydroxide, manganese hydroxide, hafnium hydroxide, lead hydroxide, zirconium nitrate, zirconium acetate, zirconium oxalate, tellurium nitrate, tellurium acetate, tellurium oxalate, ruthenium nitrate, ruthenium acetate, ruthenium oxalate, titanium nitrate, titanium acetate, titanium oxalate, manganese nitrate, manganese acetate, manganese oxalate, hafnium nitrate, hafnium acetate, hafnium oxalate, and a combination thereof.
The second precursor for forming the nickel-based lithium metal oxide may include, for example, Ni(OH)2, NiO, NiOOH, NiCO3.2Ni(OH)2.4H2O, NiC2O4.2H2O, Ni(NO3)2.6H2O, NiSO4, NiSO4.6H2O, a nickel fatty acid salt, a nickel halide, or a combination thereof.
The second precursor for forming the nickel-based lithium metal oxide may essentially include a nickel precursor (e.g., as a major component), and may further include one or more metal precursor selected from of a cobalt precursor, a manganese precursor, and an aluminum precursor.
The cobalt precursor may include one or more selected from Co(OH)2, CoOOH, CoO, Co2O3, Co3O4, Co(OCOCH3)2.4H2O, CoCl2, Co(NO3)2.6H2O, and Co(SO4)2.7H2O.
The manganese precursor may include one or more selected from manganese oxide (such as Mn2O3, MnO2, and/or Mn3O4), manganese salts (such as MnCO3, Mn(NO3)2, MnSO4, manganese acetate, manganese dicarboxylate, manganese citrate, manganese oxy hydroxide, and/or manganese fatty acid salts), and manganese halide (such as manganese chloride).
The aluminum precursor may include aluminum nitrate (Al(NO3)3), aluminum hydroxide (Al(OH)3), aluminum sulfate, and/or the like.
The lithium precursor may include a lithium hydroxide, a lithium nitrate, a lithium carbonate, a lithium acetate, a lithium sulfate, a lithium chloride, a lithium fluoride, or a mixture thereof.
Hereinafter, a method of preparing a positive active material according to another embodiment is described.
A method of preparing a positive active material for a rechargeable lithium battery according to another embodiment includes mixing a first precursor for forming (to form) lithium-metal (M) oxide, a second precursor for forming nickel-based lithium metal oxide, and a lithium precursor with a solvent to obtain a precursor composition,
adding a chelating agent to the precursor composition and mixing them to form a gel,
first heat-treating the gel to obtain a first product, and
second heat-treating the first product to obtain a second product.
First, the positive active material precursor composition is obtained by mixing the first precursor for forming the lithium-metal (M) oxide, the second precursor for forming the nickel-based lithium metal oxide, and the lithium precursor, with a solvent. Herein, water and/or suitable alcohols may be used as the solvent, and the alcohol may include ethanol, methanol, isopropanol, and/or the like.
The contents of the first precursor for forming the lithium-metal (M) oxide and the second precursor for forming the nickel-based lithium metal oxide may be suitably or properly controlled to obtain the positive active material having a desired composition.
For example, when the first precursor for forming the lithium-metal (M) oxide is included in an amount of x mole (0<x≤0.1, 0<x≤0.09, 0<x≤0.08, 0<x≤0.07, 0<x≤0.06, 0<x≤0.05, 0<x≤0.04, 0<x≤0.03, 0<x≤0.02, 0<x≤0.01, 0.01<x≤0.05, 0.02<x≤0.05, or 0.02<x≤0.03), an amount of the second precursor for forming the nickel-based lithium metal oxide is (1-x) mole, and an amount of the lithium precursor may be adjusted to have a mixing ratio of about 1.03(1+x) mole.
Subsequently, the chelating agent is added to the positive active material precursor composition and then, stirred until all the solvents are removed from the positive active material precursor composition to obtain the positive active material precursor as a gel. An amount of the chelating agent is not particularly limited but may be, for example, added to include a chelate and cations in the composition in a mole ratio of 1:1.
The chelating agent traps metal ions in the precursor composition and prevents (or reduces) localization of the metal ions, and thus facilitates the mixing. The chelating agent may include, for example, organic acid. The organic acid may be at least one selected from citric acid, acrylic acid, methacrylic acid, tartaric acid, glycolic acid, oxalic acid, ethylenediamine tetraacetic acid, and glycine.
The first heat-treating may be for example performed at a temperature of greater than or equal to about 250° C., greater than or equal to about 260° C., greater than or equal to about 270° C., greater than or equal to about 280° C., greater than or equal to about 290° C., greater than or equal to about 300° C., greater than or equal to about 310° C., greater than or equal to about 320° C. and for example less than or equal to about 400° C., less than or equal to about 390° C., less than or equal to about 380° C., less than or equal to about 370° C., less than or equal to about 360° C., less than or equal to about 350° C., less than or equal to about 340° C., or less than or equal to about 330° C. Herein, the first heat-treating may be performed within any of these temperature ranges for about 5 hours to 15 hours under a high pressure. Such first heat-treating may provide dispersion including the first precursor and the second precursor dispersed in the solvent.
The second heat-treating may be performed under an oxygen (02) atmosphere, for example, at a temperature in a range of greater than or equal to about 700° C., greater than or equal to about 710° C., greater than or equal to about 720° C., greater than or equal to about 730° C., greater than or equal to about 740° C., greater than or equal to about 750° C., greater than or equal to about 760° C., greater than or equal to about 770° C., greater than or equal to about 780° C., greater than or equal to about 790° C., or greater than or equal to about 800° C. and for example, less than or equal to about 950° C., less than or equal to about 940° C., less than or equal to about 930° C., less than or equal to about 920° C., less than or equal to about 910° C., less than or equal to about 900° C., less than or equal to about 890° C., less than or equal to about 880° C., less than or equal to about 870° C., less than or equal to about 860° C., or less than or equal to about 850° C., for about 5 to about 15 hours.
During the second heat-treating, the temperature may be adjusted depending on a nickel content of the nickel-based lithium metal oxide. In one embodiment, when the nickel content based on a total amount of metals of the nickel-based lithium metal oxide is less than or equal to about 70 mol %, the second heat-treating may be performed at greater than or equal to about 700° C., greater than or equal to about 750° C., greater than or equal to about 800° C., greater than or equal to about 850° C., or greater than or equal to about 900° C. In another embodiment, when the nickel content based on an total content of metals of the nickel-based lithium metal oxide is greater than about 70 mol %, the second heat-treating may be performed at a temperature of greater than or equal to about 700° C., greater than or equal to about 750° C., greater than or equal to about 800° C., or greater than or equal to about 850° C. and less than or equal to about 700° C., less than or equal to about 750° C., less than or equal to about 800° C., less than or equal to about 850° C., or less than or equal to about 900° C.
When the second heat-treating is performed within any of these ranges described herein, phase-separation of the lithium-metal oxide may easily occur, and the coating layer including the lithium-metal oxide may be stably (or suitably) formed on the (003) crystalline plane of the nickel-based lithium metal oxide.
In some embodiments, the temperature-increasing rate of the second heat-treating may be less than or equal to about 5° C./min, for example, less than or equal to about 4° C./min, for example, less than or equal to about 3° C./min, for example, less than or equal to about 2° C./min, or for example, less than or equal to about 1° C./min.
The cooling rate ensuing the second heat-treating may be, for example, less than or equal to about 1° C./min, for example, less than or equal to about 0.7° C./min, for example, less than or equal to about 0.5° C./min, for example, less than or equal to about 0.3° C./min, or for example, less than or equal to about 0.1° C./min.
In the method, the first precursor for forming lithium-metal (M) oxide may include a metal (M)-containing halide, a metal (M)-containing sulfate, a metal (M)-containing hydroxide, a metal (M)-containing nitrate, a metal (M)-containing carboxylate, a metal (M)-containing oxalate, or a combination thereof. Non-limiting examples of the first precursor may include tin chloride (SnCl2), zirconium chloride (ZrCl4), tellurium chloride (TeCl4), ruthenium chloride (RuCl4), titanium chloride (TiCl4), manganese chloride (MnCl4), hafnium chloride (HfCl4), lead chloride (PbCl4), tin sulfate (SnSO4), zirconium sulfate (Zr(SO4)2), tellurium sulfate (Te(SO4)2), ruthenium sulfate (Ru(SO4)2), titanium sulfate (Ti(SO4)2), manganese sulfate (Mn(SO4)2), hafnium sulfate (Hf(SO4)2), lead sulfate (Pb(SO4)2), tin hydroxide, zirconium hydroxide, tellurium hydroxide, ruthenium hydroxide, titanium hydroxide, manganese hydroxide, hafnium hydroxide, lead hydroxide, zirconium nitrate, zirconium acetate, zirconium oxalate, tellurium nitrate, tellurium acetate, tellurium oxalate, tellurium chloride, ruthenium nitrate, ruthenium acetate, ruthenium oxalate, titanium nitrate, titanium acetate, titanium oxalate, manganese nitrate, manganese acetate, manganese oxalate, hafnium nitrate, hafnium acetate, hafnium oxalate, and a combination thereof.
The second precursor for forming the nickel-based lithium metal oxide having the layered crystal structure may include, for example, Ni(OH)2, NiO, NiOOH, NiCO3.2Ni(OH)2.4H2O, NiC2O4.2H2O, Ni(NO3)2.6H2O, NiSO4, NiSO4.6H2O, a nickel fatty acid salt, a nickel halide, or a combination thereof.
The second precursor for forming the nickel-based lithium metal oxide having the layered crystal structure may essentially include a nickel precursor (e.g., as a major component), and may further include one or more metal precursor selected from of a cobalt precursor, a manganese precursor, and an aluminum precursor.
The cobalt precursor may include one or more selected from Co(OH)2, CoOOH, CoO, Co2O3, Co3O4, Co(OCOCH3)2.4H2O, CoCl2, Co(NO3)2.6H2O, and Co(SO4)2.7H2O.
The manganese precursor may include one or more selected from manganese oxide (such as Mn2O3, MnO2, and/or MnO4), manganese salts (such as MnCO3, Mn(NO3)2, MnSO4, manganese acetate, manganese dicarboxylate, manganese citrate, and/or manganese fatty acid salts), manganese oxy hydroxide, and manganese halide (such as manganese chloride).
The aluminum precursor may include aluminum nitrate (Al(NO3)3), aluminum hydroxide (Al(OH)), aluminum sulfate, and/or the like.
The lithium precursor may include a lithium hydroxide, a lithium nitrate, a lithium carbonate, a lithium acetate, a lithium sulfate, a lithium chloride, a lithium fluoride, or a mixture thereof.
When the prepared positive active material is used, a positive electrode having excellent (or suitable) chemical stability under a high temperature charge and discharge condition and a rechargeable lithium battery having excellent (or suitable) power output characteristics by using this positive electrode may be manufactured.
Hereinafter, a process of manufacturing a rechargeable lithium battery by using the above positive active material as a positive active material for a rechargeable lithium battery is examined, and herein, a method of manufacturing the rechargeable lithium battery having a positive electrode, a negative electrode, a lithium salt-containing non-aqueous electrolyte, and a separator is illustrated.
The positive electrode and negative electrode are fabricated by coating and drying each of a composition for forming a positive active material layer and a composition for forming a negative active material layer on a current collector, respectively.
The positive active material forming composition is prepared by mixing a positive active material, a conductive agent, a binder, and a solvent. The positive active material according to an embodiment is used as the positive active material for the composition.
The binder may help binding of active materials, conductive agent, and/or the like, and binding them on a current collector, and may be added in an amount of about 1 to about 50 parts by weight based on a total weight (100 parts by weight) of the positive active material. Non-limiting examples of such a binder may be polyvinylidene fluoride, polyvinyl alcohol, carboxymethyl cellulose (CMC), starch, hydroxypropyl cellulose, recycled cellulose, polyvinylpyrrolidone, polytetrafluoroethylene, polyethylene, polypropylene, an ethylene-propylene-diene terpolymer (EPDM), sulfonated EPDM, a styrene butadiene rubber, a fluorine rubber, various copolymers, and the like. The amount thereof may be about 1 part by weight to about 5 parts by weight based on a total weight (100 parts by weight) of the positive active material. When the amount of the binder is within the range described herein, the binding force of the active material layer to the current collector is good (or suitable).
The conductive agent is not particularly limited as long as it does not cause an undesirable chemical change of a battery and has conductivity (e.g., electrical conductivity), and may be, for example, graphite such as natural graphite and/or artificial graphite; a carbon-based material such as carbon black, acetylene black, ketjen black, channel black, furnace black, lamp black, summer black and/or the like; a conductive fiber such as a carbon fiber, a metal fiber, and/or the like; carbon fluoride; a metal powder such as an aluminum and/or nickel powder; zinc oxide, a conductive whisker such as potassium titanate, and/or the like; a conductive metal oxide such as a titanium oxide; and/or a conductive material such as a polyphenylene derivative and/or the like.
The amount of the conductive agent may be about 1 part by weight to about 5 parts by weight based on a total weight (100 parts by weight) of the positive active material. When the amount of the conductive agent is within the range described herein, conductivity characteristics (e.g., electrical conductivity characteristics) of the resultant electrode are improved.
Non-limiting examples of the solvent may be N-methyl pyrrolidone, and the like.
The amount of the solvent may be about 10 parts by weight to about 200 parts by weight based on 100 parts by weight of the positive active material. When the amount of the solvent is within the range described herein, the work for forming the active material layer may become easy.
The positive current collector may have a thickness of about 3 μm to about 500 μm, is not particularly limited as long as it does not cause an undesirable chemical change in the battery and has high conductivity (e.g., high electrical conductivity), and may be, for example, stainless steel, aluminum, nickel, titanium, heat-treated carbon, aluminum and/or stainless steel of which the surface is treated with carbon, nickel, titanium, and/or silver. The current collector may have fine irregularities formed on a surface thereof to increase adhesive force of the positive active material, and may have various suitable forms such as a film, a sheet, a foil, a net, a porous body, foam, and/or a non-woven fabric body.
Separately, a negative active material, a binder, a conductive agent, and a solvent are mixed to prepare a composition for a negative active material layer.
The negative active material may use a material capable of intercalating and deintercalating lithium ions. Non-limiting examples of the negative active material may be a carbon-based material (such as graphite and/or carbon), a lithium metal, an alloy thereof, a silicon oxide-based material, and the like. According to an embodiment of the present invention, silicon oxide may be used.
The binder may be added in an amount of about 1 part by weight to about 50 parts by weight based on a total weight (100 parts by weight) of the negative active material. Non-limiting examples of the binder may be the same as those for the positive electrode.
The conductive agent may be used in an amount of about 1 part by weight to about 5 parts by weight based on a total weight (100 parts by weight) of the negative active material. When the amount of the conductive agent is within the range described herein, conductivity characteristics of the resultant electrode are improved.
An amount of the solvent may be about 10 part by weight to about 200 parts by weight based on a total weight (100 parts by weight) of the negative active material. When the amount of the solvent is within the range described herein, the work for forming the negative active material layer may become easy.
The conductive agent and the solvent may use the same materials as those used in manufacturing the positive electrode.
The negative current collector may have a thickness of about 3 μm to about 500 μm. Such a negative current collector is not particularly limited as long as it does not cause an undesirable chemical change in the battery and has high conductivity (e.g., high electrical conductivity) and may be for example, copper, stainless steel, aluminum, nickel, titanium, heat-treated carbon, copper, stainless steel of which the surface is treated with carbon, nickel, titanium, silver, an aluminum-cadmium alloy, and/or the like. In addition, the negative current collector may have fine irregularities formed on a surface thereof to increase adhesive force of the negative active materials, and may have various suitable forms such as a film, a sheet, a foil, a net, a porous body, foam, and/or a non-woven fabric body, like the positive current collector.
A separator may be disposed (positioned) between the positive electrode and the negative electrode manufactured according to the above processes.
The separator may have a pore diameter of about 0.01 μm to about 10 μm and a thickness of about 5 μm to about 300 μm. Non-limiting examples may be an olefin-based polymer such as polypropylene, polyethylene, and/or the like; and a sheet and/or a nonwoven fabric formed of a glass fiber. In the case that a solid electrolyte such as a polymer is used as the electrolyte, the solid electrolyte may also serve as the separator.
A lithium salt-containing non-aqueous electrolyte may be composed of a non-aqueous electrolyte and a lithium salt. The non-aqueous electrolyte may be an aprotic organic solvent, an organic solid electrolyte, and/or inorganic solid electrolyte.
The non-aqueous electrolyte may be selected from, for example, aprotic organic solvents such as N-methyl-2-pyrrolidinone, propylene carbonate, ethylene carbonate, butylene carbonate, dimethyl carbonate, diethyl carbonate, gamma-butyro lactone, 1,2-dimethoxyethane, 2-methyl tetrahydrofuran, dimethylsulfoxide, 1,3-dioxolane, N,N-formamide, N,N-dimethyl formamide, acetonitrile, nitromethane, methyl formate, methyl acetate, trimethoxymethane, dioxolane derivative, sulfolane, methyl sulfolane, 1,3-dimethyl-2-imidazolidinone, a propylene carbonate derivative, a tetrahydrofuran derivative, ether, methyl propionate, ethyl propionate, and/or the like.
The organic solid electrolyte may be, for example, a polyethylene derivative, a polyethylene oxide derivative, a polypropylene oxide derivative, a phosphoric acid ester polymer, polyvinyl alcohol, polyvinylidene fluoride, and/or the like.
The inorganic solid electrolyte may be, for example, Li3N, LiI, Li5NI2, Li3N—LiI—LiOH, Li2SiS3, Li4SiO4, Li4SiO4—LiI—LiOH, Li3PO4—Li2S—SiS2, and/or the like.
The lithium salt may be a material which is readily soluble in the non-aqueous electrolyte, and, for example, may be LiCl, LiBr, LiI, LiClO4, LiBF4, LB10Cl10, LiPF6, LiCF3SO3, LiCF3CO2, LiAsF6, LiSbF6, LiAlCl4, CH3SO3Li, CF3SO3Li, (CF3SO2)2NLi, (FSO2)2NLi, lithium chloroborate, lower aliphatic lithium carbonate, tetraphenyl lithium borate, and/or the like
Referring to
The rechargeable lithium battery may be used for a battery cell used as a power source for small devices due to improved power output characteristics, as well as a unit battery in a medium/large battery pack, or a battery module including a plurality of battery cells used as a power source for medium/large devices.
Examples of the medium/large devices may include electric vehicles including electric vehicles (EVs), hybrid electric vehicles (HEVs), plug-in hybrid electric vehicles (PHEVs), and/or the like; electric motorcycle power tools including electric bicycles (E-bikes), electric scooters (E-scooters), and/or the like, but are not limited thereto.
Hereinafter, the embodiments are illustrated in more detail with reference to examples. These examples, however, are not in any sense to be interpreted as limiting the scope of the present disclosure.
LiOH.H2O, Ni(OH)2, Co(OH)2, and SnO2 as solid-phase powders were respectively mixed to a mole ratio of 1.08:0.76:0.19:0.05 in a mortar and then, ball-milled at 500 rpm for 2 hours to synthesize uniformly-mixed solid-phased powder.
After increasing a temperature up to 750° C., the obtained mixture was fired at 750° C. for 10 hours under an 02 atmosphere and then, cooled down to synthesize a single particle (one body) positive active material, Li[Ni0.8Co0.2]O2 plane-selectively coated with Li2SnO3 on the (003) plane. Herein, a temperature-increasing rate was set at 5° C./min, and a cooling rate was set at 1° C./min. A measured single particle diameter (D50) of the positive active material was 3.02 μm.
LiOH.H2O, Ni(OH)2, Co(OH)2, and SnO2 as solid-phase powders were respectively mixed to a mole ratio of 1.08:0.76:0.19:0.05 in a mortar and then, ball-milled at 500 rpm for 2 hours to synthesize uniformly-mixed solid-phased powder.
After increasing a temperature up to 830° C., the obtained mixture was fired at 830° C. for 10 hours under an 02 atmosphere and then, cooled down to synthesize a single particle (one body) positive active material, Li[Ni0.8Co0.2]O2 plane-selectively coated with Li8SnO6 on the (003) crystalline plane. Herein, a temperature-increasing rate was set at 5° C./min, and a cooling rate was set at 1° C./min. A measured single particle diameter (D50) of the positive active material was 2.51 μm.
LiNO3, Ni(NO3)2.6H2O, Co(NO3)2.6H2O, Al(NO3)3.9H2O, and SnCl2 in a mole ratio of Li:(Ni+Co+Al):Sn=1.08:0.95:0.05 (Ni:Co:Al=0.80:0.15:0.05) were respectively dissolved in ethanol (10 mL) to prepare a precursor composition. Subsequently, citric acid as a chelating agent was used in a mole ratio of 1:1 with cations in the precursor composition.
The obtained precursor composition was stirred, until all the solvents were removed, obtaining gel.
The obtained gel was fired at 300° C. for 5 hours in the air to obtain powder.
The temperature was increased up to 750° C., and the obtained powder was fired at 750° C. for 10 hours under an 02 atmosphere and cooled down to synthesize a single particle (one body) positive active material, Li[Ni0.80Co0.15Al0.05]O2 plane-selectively coated with Li2SnO3 on the (003) crystalline plane. Herein, a temperature-increasing rate was set at 5° C./min, and a cooling rate was set at 1° C./min. A measured single particle diameter (D50) of the positive active material was 1.68 μm.
LiNO3, Ni(NO3)2.6H2O, Co(NO3)2.6H2O, Mn(NO3)2.4H2O, and SnCl2 in a mole ratio of 1.13:0.46:0.19:0.26:0.05 were dissolved in ethanol (10 mL)) to prepare a precursor composition. Subsequently, citric acid as a chelating agent was used in a mole ratio of 1:1 with cations in the precursor composition.
The obtained solution was stirred, until all the solvents in the precursor composition were removed, obtaining gel.
The obtained gel was fired at 300° C. for 5 hours in the air to obtain powder.
The temperature was increased up to 750° C., and the obtained powder was fired at 750° C. for 10 hours under an 02 atmosphere and cooled down to synthesize a single particle (one body) positive active material, Li[Ni0.50Co0.20Mn0.30]O2 plane-selectively coated with Li2SnO3 on the (003) crystalline plane. Herein, a temperature-increasing rate was set at 5° C./min, and a cooling rate was set at 1° C./min. A measured single particle diameter (D50) of the positive active material was 1.84 μm.
LiNO3, Ni(NO3)2.6H2O, Co(NO3)2.6H2O and SnCl2 in a mole ratio of 1.13:0.76:0.19:0.05 were respectively dissolved in ethanol (10 mL) to prepare a precursor composition.
Subsequently, citric acid as a chelating agent was used in a mole ratio of 1:1 with cations in the precursor composition.
The obtained precursor composition was stirred, until all the solvents were removed, obtaining gel.
The obtained gel was fired at 300° C. for 5 hours in the air to obtain powder.
The temperature was increased up to 750° C., and the obtained powder was fired at 750° C. for 10 hours under an 02 atmosphere and cooled down to synthesize a single particle (one body) positive active material, Li[Ni0.85Co0.15]O2 plane-selectively coated with Li2SnO3 on the (003) crystalline plane.
Herein, a temperature-increasing rate was set at 5° C./min, and a cooling rate was set at 1° C./min. A measured single particle diameter (D50) of the positive active material was 1.35 μm.
LiOH.H2O, Ni(OH)2 and Co(OH)2 as solid-phase powders were respectively mixed to a mole ratio of 1.03:0.8:0.2 in a mortar and then, ball-milled at 500 rpm for 2 hours to synthesize uniformly-mixed solid-phased powder.
After increasing a temperature up to 750° C., the obtained mixture was fired at 750° C. for 10 hours under an 02 atmosphere and then, cooled down to synthesize a single particle (one body) positive active material, Li[Ni0.8Co0.2]O2.
Herein, a temperature-increasing rate was set at 5° C./min, and a cooling rate was set at 1° C./min. A measured single particle diameter (D50) of the positive active material was 2.81 μm.
LiNO3, Ni(NO3)2.6H2O, and Co(NO3)2.6H2O in a mole ratio of 1.03:0.8:0.2 were dissolved in ethanol (10 mL) to prepare a precursor composition. Subsequently, citric acid as a chelating agent was used in a mole ratio of 1:1 with cations in the precursor composition.
The obtained solution was stirred, until all the solvents in the precursor composition were removed, obtaining gel.
The obtained gel was fired at 300° C. for 5 hours in the air to obtain powder.
The temperature was increased up to 750° C., and the obtained powder was fired at 750° C. for 10 hours under an 02 atmosphere and cooled down to synthesize Li[Ni0.80Co0.20]O2. Herein, a temperature-increasing rate was set at 5° C./min, and a cooling rate was set at 1° C./min.
LiNO3 and tin (IV) ethylhexanoisopropoxide (Sn—(OOC8H15)2(OC3H7)2) in a mole ratio of 2:1 were dissolved in 2-propanol (IPA), and the synthesized Li[Ni0.80Co0.20]O2 was dispersed in the solution and then, stirred at room temperature for about 20 hours to evaporate the solvent and thus obtain gel.
The obtained gel was fired at 150° C. for 10 hours to obtain powder.
The temperature was increased up to 700° C., and the obtained powder was fired at 700° C. for 5 hours and then, cooled down to obtain a positive active material, Li[Ni0.8Co0.2]O2 coated with Li2SnO3. Herein, a temperature-increasing rate was set at 10° C./min, and a cooling rate was set at 1° C./min.
The positive active material includes secondary particle in which a plurality of primary particles are aggregated. The particle size of the primary particles was 500 nm, and the particle size (D50) of the secondary particles was 8.23 μm.
LiNO3, Ni(NO3)2.6H2O, Co(NO3)2.6H2O, and Al(NO3)3.9H2O in a mole ratio of 1.03:0.80:0.15:0.05 were dissolved in ethanol (10 mL) to prepare a precursor composition. Subsequently, citric acid as a chelating agent was used in a mole ratio of 1:1 with cations in the precursor composition.
The obtained solution was stirred, until all the solvents in the precursor composition were removed, obtaining gel.
The obtained gel was fired at 300° C. for 5 hours in the air to obtain powder.
The temperature was increased up to 750° C., and the obtained powder was fired at 750° C. for 10 hours under an 02 atmosphere and cooled down to synthesize Li[Ni0.80Co0.15Al0.05]O2 positive active material. Herein, a temperature-increasing rate was set at 5° C./min, and a cooling rate was set at 1° C./min.
The positive active material includes secondary particle in which a plurality of primary particles are aggregated. The particle size of the primary particles was 125 nm, and the particle size (D50) of the secondary particles was greater than or equal to 7.78 μm.
LiNO3, Ni(NO3)2.6H2O, Co(NO3)2.6H2O, and Mn(NO3)2.4H2O in a mole ratio of 1.03:0.5:0.2:0.3 were dissolved in ethanol (10 mL) to prepare a precursor composition. Subsequently, citric acid as a chelating agent was used in a mole ratio of 1:1 with cations in the precursor composition.
The obtained solution was stirred, until all the solvents in the precursor composition were removed, obtaining gel.
The obtained gel was fired at 300° C. for 5 hours in the air to obtain powder.
The temperature was increased up to 800° C., and the obtained powder was fired at 800° C. for 10 hours under an 02 atmosphere and then, cooled down to synthesize Li[Ni0.5Co0.2Mn0.3]O2 positive active material. Herein, a temperature-increasing rate was set at 5° C./min, and a cooling rate was set at 1° C./min.
The positive active material includes secondary particle in which a plurality of primary particles are aggregated. The particle size of the primary particles was 125 nm, and the particle size (D50) of the secondary particles was greater than or equal to 4.20 μm.
LiNO3, Ni(NO3)2.6H2O, and Co(NO3)2.6H2O in a mole ratio of 1.03:0.8:0.2 were dissolved in ethanol (10 mL) to prepare a precursor composition. Subsequently, citric acid as a chelating agent was used in a mole ratio of 1:1 with cations in the precursor composition.
The obtained solution was stirred, until all the solvents in the precursor composition were removed, obtaining gel.
The obtained gel was fired at 300° C. for 5 hours in the air to obtain powder.
The temperature was increased up to 750° C., and the obtained powder was fired at 750° C. for 10 hours under an 02 atmosphere and cooled down to synthesize Li[Ni0.80Co0.20]O2. Herein, a temperature-increasing rate was set at 5° C./min, and a cooling rate was set at 1° C./min.
The positive active material includes secondary particle in which a plurality of primary particles are aggregated. The particle size of the primary particles was 500 nm, and the particle size (D50) of the secondary particles was 7.56 μm.
The positive active material for a rechargeable lithium battery according to Synthesis Example 1 was used to manufacture a coin cell.
The Li[Ni0.8Co0.2]O2 positive active material according to Synthesis Example 1, Super-p (TIMCAL) as a conductive agent, and polyvinylidene fluoride (PVdF) as a binder were mixed in a mole ratio of 0.80:0.10:0.10, and N-methyl pyrrolidone (NMP) was added thereto and uniformly dispersed therein to prepare slurry for a positive active material layer.
The prepared slurry was coated on an aluminum foil by using a doctor blade to form a thin electrode plate and then, dried at 100° C. for greater than or equal to 3 hours and at 120° C. for 10 hours in a vacuum oven to remove moisture and thus manufacture a positive electrode.
The positive electrode and a lithium metal negative electrode were used to manufacture a 2032 type coin cell. Herein, a separator formed of a porous polyethylene (PE) film (a thickness: about 20 μm) was disposed between the positive electrode and the lithium metal counter electrode, and an electrolyte was injected thereinto to manufacture the coin cell.
Herein, the electrolyte was prepared by dissolving 1.3 M LiPF6 in a mixed solvent of ethylenecarbonate (EC), ethylmethylcarbonate (EMC), and dimethylcarbonate (DMC) in a volume ratio of 3:4:3.
Rechargeable lithium battery cells according to Examples 2 to 5 were manufactured according to the same (or substantially the same) method as Example 1 except that each positive active material according to Synthesis Examples 2 to 5 was respectively used instead of the positive active material according to Synthesis Example 1.
Rechargeable lithium battery cells according to Comparative Examples 1 to 5 were manufactured according to the same (or substantially the same) method as Example 1 except that each positive active material according to Comparative Synthesis Examples 1 to 5 was respectively used instead of the positive active material according to Synthesis Example 1.
An XRD analysis of each positive active material according to Synthesis Example 1, Synthesis Example 2, Synthesis Example 3, Comparative Synthesis Example 1, and Comparative Synthesis Example 3 was carried out. The XRD analysis was performed by using a Bruker D8 Advance X-ray diffractometer with Cu Kα radiation (λ=1.5406 Å), and the XRD analysis results are shown in
Referring to
Referring to
Accordingly, in the XRD analysis results of
A STEM-EDS (scanning transmission electron microscopy-energy dispersive X-ray spectroscopy) analysis of the positive active material according to Synthesis Example 1 was performed. The STEM-EDS analysis was performed by using a JEM-ARM200F microscope made by JEOL Ltd., and the analysis results are shown in
A sample was prepared by cutting the cross section of particles with an Ar ion-slicer to examine a coating formation result with STEM. The results are shown in
Referring to
STEM-HAADF (Scanning Transmission Electron Microscope-high-Angle Annular Dark Field) and Fast Fourier Transformation (FFT) analyses of the positive active material according to Synthesis Example 1 were performed. The STEM-HAADF and FFT analyses were performed by using a JEM-ARM200F microscope made by JEOL Ltd.
The STEM-HAADF and FFT analysis results were shown in
Referring to
Power output characteristics of each cell according to Example 1, Example 2, Comparative Example 1, and Comparative Example 2 were evaluated according to the following method.
The coin cells according to Example 1, Example 2, Comparative Example 1 and Comparative Example 2 were charged under a constant current to 4.3 V at a rate of 0.1 C in the 1st cycle and then, discharged under a constant current to 2.7 V at a rate of 0.1 C. At this time, it proceeded with a current density of 20 mA g−1 at 0.1 C. The 2nd cycle and the 3rd cycle were repetitively performed under the same condition as the 1st cycle.
The 4th cycle was performed by charging the coin cells under a constant current to 4.3 V at a rate of 0.5 C and discharging them under a constant current to 2.7 V at a rate of 0.5 C after the 3rd cycle. The 5th cycle and the 6th cycle were repetitively performed under the same condition as that of the 4th cycle.
The 7th cycle was performed by charging the coin cells under a constant current to 4.3 V at 1 C and then discharging them under a constant current to 2.7 V at a rate of 1 C after the 6th cycle. The 8th cycle and the 9th cycle were repetitively performed under the same condition as that of the 7th cycle.
The 10th cycle was performed by charging the coin cells under a constant current to 4.3 V at 3.0 C and then discharging them under a constant current to 2.7 V at a rate of 3.0 C after the 9th cycle. The 11th cycle and the 12th cycle were repetitively performed under the same condition as that of the 10th cycle.
The 13th cycle was performed by charging the coin cells under a constant current to 4.3 V at 5.0 C and then discharging them under a constant current to 2.7 V at a rate of 5.0 C after the 12th cycle. The 14th cycle and the 15th cycle were repetitively performed under the same condition as that of the 13th cycle.
The 16th cycle was performed by charging the coin cells under a constant current to 4.3 V at 7.0 C and then discharging them under a constant current to 2.7 V at a rate of 7.0 C after the 15th cycle. The 17th cycle and the 18th cycle were repetitively performed under the same condition as that of the 16th cycle.
The 19th cycle was performed by charging the coin cells under a constant current to 4.3 V at 10.0 C and then discharging them under a constant current to 2.7 V at a rate of 10.0 C after the 18th cycle. The 20th cycle and the 21st cycle were repetitively performed under the same condition as that of the 19th cycle.
Power output characteristics of the coin cells according to Example 1, Example 2, Comparative Example 1 and Comparative Example 2 are shown in Table 2 and
Referring to these results, the coin cells of Example 1 and Example 2 exhibited higher discharge capacity retention at a high rate of 1.0 C compared with those of Comparative Example 1 and Comparative Example 2. Accordingly, the coin cells according to Example 1 and Example 2 exhibited improved power output characteristic compared with the coin cells according to Comparative Example 1 and Comparative Example 2.
Power output characteristics of each cell according to Example 3 and Comparative Example 3 were evaluated according to the following method.
The coin cells according to Example 3 and Comparative Example 3 were charged under a constant current to 4.4 V at a rate of 0.1 C in the 1st cycle and then, discharged under a constant current to 3.0 V at a rate of 0.1 C. The 2nd cycle and the 3rd cycle were repetitively performed under the same condition as the 1st cycle.
The 4th cycle was performed by charging the coin cells under a constant current to 4.3 V at a rate of 0.5 C and discharging them under a constant current to 2.7 V at a rate of 0.5 C after the 3rd cycle. The 5th cycle and the 6th cycle were repetitively performed under the same condition as that of the 4th cycle.
The 7th cycle was performed by charging the coin cells under a constant current to 4.3 V at 1 C and then discharging them under a constant current to 2.7 V at a rate of 1 C after the 6th cycle. The 8th cycle and the 9th cycle were repetitively performed under the same condition as that of the 7th cycle.
The 10th cycle was performed by charging the coin cells under a constant current to 4.3 V at 3.0 C and then discharging them under a constant current to 2.7 V at a rate of 3.0 C after the 9th cycle. The 11th cycle and the 12th cycle were repetitively performed under the same condition as that of the 10th cycle.
The 13th cycle was performed by charging the coin cells under a constant current to 4.3 V at 5.0 C and then discharging them under a constant current to 2.7 V at a rate of 5.0 C after the 12th cycle. The 14th cycle and the 15th cycle were repetitively performed under the same condition as that of the 13th cycle.
The 16th cycle was performed by charging the coin cells under a constant current to 4.3 V at 7.0 C and then discharging them under a constant current to 2.7 V at a rate of 7.0 C after the 15th cycle. The 17th cycle and the 18th cycle were repetitively performed under the same condition as that of the 16th cycle.
The 19th cycle was performed by charging the coin cells under a constant current to 4.3 V at 10.0 C and then discharging them under a constant current to 2.7 V at a rate of 10.0 C after the 18th cycle. The 20th cycle and the 21st cycle were repetitively performed under the same condition as that of the 19th cycle.
Power output characteristics of the coin cells according to Example 3 and Comparative Example 3 are shown in Table 3 and
Referring to these results, the coin cell of Example 3 exhibited higher discharge capacity retention at a high rate of 1.0 C compared with that of Comparative Example 3. Accordingly, the coin cell according to Example 3 exhibited improved power output characteristic compared with the coin cell according to Comparative Example 3.
Power output characteristics of each cell according to Example 4 and Comparative Example 4 were evaluated according to the following method.
The coin cells according to Example 4 and Comparative Example 4 were charged under a constant current to 4.4 V at a rate of 0.1 C in the 1st cycle and then, discharged under a constant current to 3.0 V at a rate of 0.1 C. The 2nd cycle and the 3rd cycle were repetitively performed under the same condition as the 1st cycle.
The 4th cycle was performed by charging the coin cells under a constant current to 4.4 V at a rate of 0.5 C and discharging them under a constant current to 3.0 V at a rate of 0.5 C after the 3rd cycle. The 5th cycle and the 6th cycle were repetitively performed under the same condition as that of the 4th cycle.
The 7th cycle was performed by charging the coin cells under a constant current to 4.4 V at 1.0 C and then discharging them under a constant current to 3.0 V at a rate of 1.0 C after the 6th cycle. The 8th cycle and the 9th cycle were repetitively performed under the same condition as that of the 7th cycle.
The 10th cycle was performed by charging the coin cells under a constant current to 4.4 V at 5.0 C and then discharging them under a constant current to 3.0 V at a rate of 5.0 C after the 9th cycle. The 11th cycle and the 12th cycle were repetitively performed under the same condition as that of the 10th cycle.
The 13th cycle was performed by charging the coin cells under a constant current to 4.4 V at 7.0 C and then discharging them under a constant current to 3.0 V at a rate of 7.0 C after the 12th cycle. The 14th cycle and the 15th cycle were repetitively performed under the same condition as that of the 13th cycle.
The 16th cycle was performed by charging the coin cells under a constant current to 4.4 V at 10.0 C and then discharging them under a constant current to 3.0 V at a rate of 10.0 C after the 15th cycle. The 17th cycle and the 18th cycle were repetitively performed under the same condition as that of the 16th cycle.
Power output characteristics of the coin cells according to Example 4 and Comparative Example 4 are shown in Table 4 and
Referring to these results, the coin cell of Example 4 exhibited higher discharge capacity retention at a high rate of 1.0 C compared with that of Comparative Example 4. Accordingly, the coin cell according to Example 4 exhibited improved power output characteristic compared with the coin cell according to Comparative Example 4.
The terminology used herein is for the purpose of describing particular example embodiments only and is not intended to limit the example embodiments described herein.
As used herein, the singular forms “a,” “an,” and “the” are intended to include the plural forms as well, unless the context clearly indicates otherwise.
It will be further understood that the terms “includes,” “including,” “comprises,” and/or “comprising,” when used in this specification, specify the presence of stated features, steps, operations, elements, and/or components, but do not preclude the presence or addition of one or more other features, steps, operations, elements, components, and/or groups thereof.
As used herein, expressions such as “at least one of”, “one of”, and “selected from”, when preceding a list of elements, modify the entire list of elements and do not modify the individual elements of the list.
As used herein, the term “and/or” includes any and all combinations of one or more of the associated listed items.
Further, the use of “may” when describing embodiments of the present disclosure refers to “one or more embodiments of the present disclosure”.
As used herein, the terms “substantially”, “about”, and similar terms are used as terms of approximation and not as terms of degree, and are intended to account for the inherent deviations in measured or calculated values that would be recognized by those of ordinary skill in the art.
Any numerical range recited herein is intended to include all sub-ranges of the same numerical precision subsumed within the recited range. For example, a range of “1.0 to 10.0” is intended to include all subranges between (and including) the recited minimum value of 1.0 and the recited maximum value of 10.0, that is, having a minimum value equal to or greater than 1.0 and a maximum value equal to or less than 10.0, such as, for example, 2.4 to 7.6. Any maximum numerical limitation recited herein is intended to include all lower numerical limitations subsumed therein and any minimum numerical limitation recited in this specification is intended to include all higher numerical limitations subsumed therein. Accordingly, Applicant reserves the right to amend this specification, including the claims, to expressly recite any sub-range subsumed within the ranges expressly recited herein.
As used herein, the term “major component” refers to a component that is present in a composition, polymer, or product in an amount greater than an amount of any other single component in the composition or product. In contrast, the term “primary component” refers to a component that makes up at least 50% (wt % or at %) or more of the composition, polymer, or product.
While this invention has been described in connection with what is presently considered to be practical example embodiments, it is to be understood that the invention is not limited to the disclosed embodiments. On the contrary, it is intended to cover various modifications and equivalent arrangements included within the spirit and scope of the appended claims and their equivalents.
| Number | Date | Country | Kind |
|---|---|---|---|
| 10-2019-0049393 | Apr 2019 | KR | national |
| 10-2019-0058373 | May 2019 | KR | national |
| 10-2020-0039301 | Mar 2020 | KR | national |
