Patent Application
20140023935
The present invention relates to a lithium secondary cell having high energy density and long cell life.
A lithium secondary cell has been widely used in potable electronic devices or personal computers, and is intensively studied for miniaturization and weight lightening as well as an increase in energy density.
There are several methods to increase the energy density of such a lithium secondary cell, and among others, a method of raising a cell operating voltage is effectively used. In case of a lithium secondary cell using lithium cobalt oxide or lithium manganate as a positive electrode active substance, an average operating voltage is 3.6˜3.8V (4V class) with respect to metallic lithium. This operating voltage is determined by the redox reaction of Co ion or Mn ion (Co3+←→Co4+ or Mn3+←→Mn4+).
In contrast, a spinel compound in which some of Mn in lithium manganate is substituted with a component such as nickel, for example LiNi0.5Mn1.5O4 shows a potential plateau in an area above 4.5V and such spinel compounds may be used as a positive electrode active substance to achieve an operating voltage of 5V class. For a positive electrode using a spinel compound, Mn is present as Mn4+ state, and a cell operating voltage is determined by the redox reaction of Ni2+←→Ni4+ rather than the redox reaction of Mn3+←→Mn4+.
The compound LiNi0.5Mn1.5O4 has a capacity of 130 mAh/g or higher, and an average operating voltage is 4.6V or higher with respect to metallic lithium. This compound has a lithium absorbing capacity smaller than LiCoO2 but energy density greater than LiCoO2. Thus, LiNi0.5Mn1.5O4 is useful for a positive electrode material.
However, since cells using positive electrode active substances having high potential such as LiNi0.5Mn1.5O4 shows operating voltages higher than cells using substances such as LiCoO2 or LiMn2O4 as a positive electrode active substance, the portions of an electrolytic solution that comes in contact with a positive electrode may be easily degraded. A cell capacity is greatly reduced during charge/discharge cycles or in charge state. In particular, when a cell is used under high-temperature environments, the degradation of an electrolytic solution is largely increased. There is a need to improve cell life when operating at a high temperature above 40° C., as well as to develop an electrolytic solution having high voltage-resistance and long cell life even when used under high-temperature environments for cells having high operating voltages.
To prepare cells of high capacity and low costs, a carbonaceous material is suitably used as a negative electrode active substance of a large cell. Among others, a cell using graphite as a negative electrode active substance has high energy density relative to amorphous carbon, and is suitable for cells having high operating voltages due to such high energy density. However, since graphite has high reactivity to electrolytic solution, it is considered as a material that causes capacity reduction, for example cells using propylene carbonate as a common electrolytic solution. Therefore, for a cell using graphite as a negative electrode active substance, an electrolytic solution having less degradation should be selected.
Specifically, Patent Document 1 discloses a nonaqueous electrolyte secondary cell using a positive electrode of which full charge state voltage is 4.4˜4.6V with respect to metallic lithium, a graphite negative electrode of which surface is coated with amorphous carbons, and a fluorine-substituted cyclic carbonate electrolytic solution. Further, Patent Document 2 discloses a nonaqueous secondary cell using a negative electrode active substance comprising graphite particles on which amorphous carbons are attached, and an electrolytic solution comprising propylene carbonate. However, when secondary cells disclosed in said Patent Documents are used with a positive electrode active substance of which saturated charge state voltage is 4.7V or higher with respect to metallic lithium, cell life is reduced due to the degradation of electrolytic solution. Therefore, there is a need for an additional improvement in these cells.
Additionally, Patent Document 3 discloses a secondary cell using a positive electrode made of an active substance such as LiNi0.5Mn1.5O4 operating at a high voltage, an amorphous carbon negative electrode, and an electrolytic solution comprising a high dielectric solvent and at least one solvent among dimethyl carbonate and ethyl carbonate. Patent Document 4 discloses a nonaqueous electrolyte cell using a positive electrode active substance represented by LixMyMn2-yO4 (0≦x≦1, 0.45≦y≦0.6), a non-graphitizable carbon negative electrode, and propylene carbonate. However, cells disclosed in said Patent Documents has low efficiency during primary charge/discharge. Therefore, there is a need for an additional improvement in energy density in these cells.
In the field of a lithium secondary cell of 5V class having a positive electrode operating voltage above 4.5V with respect to metallic lithium, there is a need for a lithium secondary cell which has high energy density, inhibits the degradation of an electrolytic solution that comes in contact with a positive electrode and a negative electrode, and has particularly long cell life when used under high-temperature environments.
It is an objective of the present invention to provide a lithium secondary cell of 5 V class having a positive electrode operating voltage of 4.5V or higher with respect to metallic lithium; the lithium secondary cell has high energy density, inhibits the degradation of an electrolytic solution that comes in contact with a positive electrode and a negative electrode, and has particularly long cell life when used under high-temperature environments.
According to the present invention, provided is a lithium secondary cell: wherein
a positive electrode comprises a lithium-manganese compound oxide represented by formula (1) as a positive electrode active substance:
Lia(M×Mn2-x-yXy)(O4-wZw) (1)
(wherein M represents one or two or more selected from Co, Ni, Fe, Cr and Cu; X represents one or two or more selected from Li, B, Na, Mg, Al, Ti, Si, K and Ca; Z represents one or two selected from F and Cl; and x, y and z represent numerical values satisfying 0.4≦x≦1.2, 0≦y, x+y<2, 0≦a≦1.2, 0≦w≦1); a negative electrode comprises graphite of which surface is coated by low-crystallinity carbon as a negative electrode active substance; and an electrolytic solution comprises one or two or more high-oxidation-potential solvents selected from propylene carbonate, butylene carbonate, 4-fluoro-1,3-dioxolane-2-one and 4,5-difluoro-1,3-dioxolane-2-one within a range of 5 vol % to 60 vol % of the solvent of the electrolytic solution and one or two low-viscosity solvents selected from dimethyl carbonate and fluorinated chain-type ether.
The lithium secondary cell according to the present invention includes lithium secondary cells of 5V class having a positive electrode operating voltage of 4.5V or higher with respect to metallic lithium wherein the lithium secondary cell has high energy density, inhibits the degradation of an electrolytic solution that comes in contact with a positive electrode and a negative electrode, and has particularly long cell life when it is used under high-temperature environments.
The lithium secondary cell according to the present invention has a positive electrode, a negative electrode, and an electrolytic solution in which the positive electrode and the negative electrode are immersed.
The positive electrode contains a positive electrode active substance, as well as has a structure that the positive electrode active substance is bonded on a positive electrode current collector by a binding agent for positive electrode.
The positive electrode active substance emits lithium ions into an electrolytic solution during charge and absorbs lithium ions in the electrolytic solution during discharge, and comprises a lithium manganese oxide complex represented by formula (1).
Lia(MxMn2-x-yXy)(O4-wZw) (1)
In the formula (1), M represents one or two or more selected from Co, Ni, Fe, Cr and Cu; X represents one or two or more selected from Li, B, Na, Mg, Al, Ti, Si, K and Ca; Z represents one or two selected from F and Cl; and x, y and z represent numerical values satisfying 0.4≦x≦1.2, 0≦y, x+y<2, 0≦a≦1.2, 0≦w≦1.
In the formula (1), M may be substituted with Mn. To obtain a high capacity active substance having high energy density, it is preferred that M is Ni. If M represents only Ni, it is preferred that x represents values between 0.4 and 0.6 to obtain a lithium-manganese oxide complex of high energy density, and more preferably x is 0.5. “a” satisfies 0≦a≦1.2, and preferably “a” represents 0<a≦1. Specifically LiNi0.5Mn1.5O4 has high energy density and a lithium absorbing capacity of 130 mAh/g or higher.
In the formula (1), X represents one or two or more elements selected from Li, B, Na, Mg, Al, Ti, Si, K and Ca that may be substituted with Mn. When a lithium-manganese oxide complex contains these elements, the lithium-manganese oxide complex may have prolonged life with respect to charge/discharge of a cell. Among others, it is preferred to contain at least one of Al, Mg, Ti and Si in terms of prolonged life of the lithium-manganese compound oxide, and in particular, for high capacity and long life of the cell, the lithium-manganese oxide complex contains preferably Ti. “y” is preferably greater than 0 but not more than 0.3. If “y” is not more than 0.3, the lowering of cell capacity may be suppressed.
In the formula (1), Z represents one or two elements selected from F and Cl that may be substituted with O. When a lithium-manganese oxide complex contains these elements, the lowering of cell capacity may be suppressed, “w” is preferably greater than 0 but not more than 1.
The lithium-manganese oxide complex represented by the formula (1) is spinel compound, so an operating voltage thereof is 4.5 V or higher with respect to metallic lithium.
For the lithium-manganese oxide complex represented by the formula (1), a specific surface area thereof may be for example 0.01˜5 m2/g, preferably 0.05˜4 m2/g, more preferably 0.1˜3 m2/g, and even more preferably 0.2˜2 m2/g. When the specific surface area is within the ranges indicated above, an area that comes in contact with an electrolytic solution may be suitably modulated. If the specific surface area of a lithium-manganese oxide complex is at least 0.01 m2/g, lithium ions are readily emitted and absorbed in a positive electrode during charge/discharge, and resistance may be more reduced. Also, if the specific surface area of a lithium-manganese oxide complex is not more than 5 m2/g, the degradation of an electrolytic solution and leakage of active substance components into the electrolytic solution may be suppressed.
The specific surface area of the lithium-manganese oxide complex may be measured using a gas adsorption type specific surface area-measuring device.
A median particle size of the lithium-manganese oxide complex is preferably 0.1˜50 μm, and more preferably 0.2˜40 μm. If the median particle size of the lithium-manganese oxide complex is at least 0.1 μm, the leakage of components such as Mn into an electrolytic solution and degradation of a positive electrode due to contact with the electrolytic solution may be suppressed. Also, the median particle size of the lithium-manganese compound oxide complex is not more than 50 μm, lithium ions are readily emitted and absorbed in the positive electrode during charge/discharge, and resistance may be more reduced.
The median particle size of the lithium-manganese oxide complex may be measured using a laser diffraction/scattering particle size distribution-measuring device.
The lithium-manganese oxide complex represented by the formula (1) may be prepared by weighing a metal oxide such as MnO2 or NiO and a lithium compound such as lithium carbonate at a desired metal composition ratio, grinding and mixing, and firing at a firing temperature, for example at a temperature of 500˜1000° C. By modulating a faring time, fine particles having specific surface areas indicated above might be obtained.
Also, the positive electrode active substance may further comprise other active substances as long as they do not adversely affect the lithium-manganese oxide complex represented by the formula (1). Examples of other active substances may include LiM1xMn2-xO4 (M1: elements other than Mn, 0<x<0.4), LiCoO2, Li(M2xMn1-x)O2(M2: elements other than Mn), Li(M3xNi1-x)O2, (M3: elements other than Ni), LiM4PO4 (M4: including at least Fe, Co, Mn, or Ni), Li2MSiO4 (M: at least one of Mn, Fe, Co), or the like. They may be used alone or as any combination of two or more species.
To bind the positive electrode active substance, a binding agent for positive electrode is used. Examples of the binding agent for positive electrode may include polyvinylidene fluoride (PVdF), vinylidene fluoride-hexafluoropropylene copolymer, vinylidene fluoride-tetrafluoroethylene copolymer, styrene-butadiene copolymer rubber, polytetrafluoroethylene, polypropylene, polyethylene, polyimide, polyamideimide, or the like. Among others, polyvinylidene fluoride is preferred in terms of generality or low costs. An amount of the binding agent used is preferably 2˜10 parts by weight with respect to 100 parts by weight of the positive electrode active substance in terms of “sufficient binding ability” and “high energization” that are traded off against each other.
The positive electrode current collector acts to support a positive electrode active substance layer containing the positive electrode active substance bonded by a binding agent, and should have conductivity to transmit electricity to an external terminal Aluminum, nickel, copper, silver or alloys thereof is preferably used in terms of electrochemical stability. The positive electrode current collector may have any form of foil, flat plate, mesh or the like.
To reduce impedance of the positive electrode active substance, the positive electrode active substance layer may further contain electroconductive-assisting additives.
Examples of electroconductive-assisting additives may include carbonaceous particulates such as graphite, carbon black or acetylene black.
The positive electrode may be fabricated onto the positive electrode current collector using materials suitable for the positive electrode active substance layer containing the positive electrode active substance and the binding agent for positive electrode. A method of preparing the positive electrode active substance layer may be any of coating methods such as a doctor blade method, a die coater method, a CVD method, a sputtering method or the like. Alternatively, the positive electrode active substance layer may be previously formed, and then a thin layer of aluminum, nickel or alloys thereof may be formed thereon by a method such as vapor deposition or sputtering to obtain a positive electrode current collector.
The negative electrode contains a negative electrode active substance, as well as has a structure that the negative electrode active substance is bonded on a negative electrode current collector by a binding agent for negative electrode.
The negative electrode active substance absorbs lithium ions in an electrolytic solution during charge and emits lithium ions into the electrolytic solution during discharge, and it comprises graphite of which surface is coated by low-crystallinity carbon. By using high-crystallinity graphite of which surface is coated by low-crystallinity carbon as the negative electrode active substance, even when the negative electrode contains highly electroconductive graphite, the resulting negative electrode may have high energy density, low reaction with the electrolytic solution, and high cell capacity.
A crystal structure of graphite has preferably 0.33 to 0.34 nm of layer spacing in 002 face d002, more preferably 0.333 to 0.337 nm, and even more preferably up to 0.336 nm. Such high-crystallinity graphite has high lithium absorbing capacity, resulting in enhancing charge/discharge efficiency.
The layer spacing of graphite may be measured using X-ray diffraction.
Preferably, the low-crystallinity carbon that coats the surface of the graphite has not less than 0.08 and not more than 0.5 of a ratio of the intensity of D peak (ID) that is emerged in the range of 1300 cm−1 to 1400 cm−1 to the intensity of G peak (IG) that is emerged in the range of 1550 cm−1 to 1650 cm−1 (ID/IG) in a Raman spectrum of Laser Raman Analysis. High-crystallinity carbons have low ID/IG values, while low-crystallinity carbons have high ID/IG values. If the ID/IG is at least 0.08, the reaction between the electrolytic solution and the graphite operating a high voltage may be suppressed, and cell life may be prolonged. Also, if the ID/IG is not more than 0.5, the lowering of cell capacity may be suppressed. More preferably, the ID/IG of the low-crystallinity carbon that covers the surface of the graphite is not less than 0.1 and not more than 0.4.
For Laser Raman Analysis of the low-crystallinity carbon, the graphite coating with the low-crystallinity carbon may be measured using Argon ion laser Raman Analyzer. In case of a material having high laser absorption such as carbon, laser is absorbed in several tens nm from the surface of the material. Thus, when the graphite coating with the low-crystallinity carbon is subjected to Laser Raman Analysis, a measurement value may substantially be that of the low-crystallinity carbon on the surface of graphite.
The ID/IG value may be calculated from Laser Raman Spectrum measured according to the following conditions.
Laser Raman Spectroscope: Ramanor T-64000 (Jobin Yvon: manufactured by Atago Co., Ltd.)
Measurement mode: Macro Raman
Measurement arrangement: 60°
Beam size: 100 μm
Light source: Ar+Laser (514.5 nm)
Laser power: 10 mW
Diffraction lattice: Single 600 gr/mm
Dispersion: Single 21 A/mm
Slit: 100 μm
Detector: CCD (Jobin Yvon1024256).
For the graphite coating with the low-crystallinity carbon, for example, the specific surface area thereof may be 0.01˜20 m2/g, preferably 0.05˜10 m2/g, more preferably 0.1˜5 m2/g, and even more preferably 0.2˜3 m2/g. When the specific surface area is within these ranges, an area that comes in contact with an electrolytic solution may be suitably modulated. If the specific surface area of the graphite coating by the low-crystallinity carbon is at least 0.01 m2/g, lithium ions are readily emitted and absorbed during charge/discharge, as well as resistance may be more reduced. Also, if the specific surface area is not more than 20 m2/g, the degradation of the electrolytic solution and the leakage of active substance components into the electrolytic solution may be suppressed.
For the graphite coating with the low-crystallinity carbon, an average particle size of graphite particles is preferably 5 to 30 μm, and a coating thickness of the low-crystallinity carbon is preferably 0.0.1 to 5 μm in terms of high energy density and low reaction with an electrolytic solution.
The average particle size may be measured using a laser diffraction/scattering particle size/particle size distribution-measuring device, for example Microtrack MT3300EX (Nikkiso Co., Ltd.).
Such the graphite coating by the low-crystallinity carbon may be prepared by various methods, such as a gaseous method of depositing carbons generated in thermal degeneration of hydrocarbons such as propane or acetylene on the surfaces of graphite particles having the average particle sizes indicated above, or a method of depositing pitch or tar on the surface of graphite and firing at 800˜1500° C.
The negative electrode active substance may further comprise other active substances as long as they do not adversely affect the low-crystallinity carbon-coating graphite. Examples of other active substances may include metals such as Al, Si, Pb, Sn, Zn, Cd, Sb, In, Bi, Ag, Ba, Ca, Hg, Pd, Pt, Te or La, alloys of two or more species thereof, or alloys of these metals or alloys and lithium. Also, examples may include silicon oxide, aluminum oxide, tin oxide, indium oxide, zinc oxide, lithium oxide, or composites thereof, metal oxides such as LiFe2O3, WO2, MoO2, SiO, SiO2, CuO, SnO, SnO2, Nb3O5, LixTi2-xO4 (1≦x≦4/3), PbG2 or Pb2O5, metal sulfides such as SnS or FeS2, polyacene or polythiophene, lithium nitrides such as Li5(Li3N), Li7MnN4, Li3FeN2, Li2.5Co0.5N and Li3CoN, or the like.
To bind the negative electrode active substance, a binding agent for negative electrode is used. Specifically, the same things as the binding agent for positive electrode indicated above may be used as the binding agent for negative electrode. An amount of the binding agent for negative electrode used is preferably 1˜30% by weight with respect to the total amount of the negative electrode active substance and the binding agent for negative electrode, and more preferably 2˜25% by weight. If the content of the binding agent for negative electrode is at least 1 wt %, it is possible to achieve better adhesion between active substances or between the active substance and the current collector and good cycle property. Also, if the content is not more than 30 wt %, the rate of active substance is increased, resulting in increasing the capacity of the negative electrode.
The negative electrode current collector acts to support a negative electrode active substance layer containing the negative electrode active substance bonded by a binding agent, and should have conductivity to transmit electricity to an external terminal. Specifically, the same things as the positive electrode current collector indicated above may be used.
The negative electrode may be fabricated onto the negative electrode current collector using a material for the negative electrode active substance layer containing the negative electrode active substance and the binding agent for negative electrode. The same methods as methods of preparing the positive electrode active substance layer may be used to prepare the negative electrode active substance layer.
The electrolytic solution enables to absorb and emit lithium in the positive electrode and the negative electrode during charge/discharge. The electrolytic solution may be prepared by dissolving an electrolyte in a lithium ion-soluble non-aqueous organic solvent, and the positive electrode and the negative electrode are immersed therein.
The solvent of the electrolytic solution comprises high oxidation potential solvents and low-viscosity solvents. If the electrolytic solution contains a high oxidation potential solvent, the degradation of the electrolytic solution is suppressed even in a high voltage cell of which operating voltage is 4.6V or more with respect to metallic lithium, and cell life may be prolonged. The high oxidation potential solvents include one or two or more selected from propylene carbonate, butylenes carbonate, 4-fluoro-1,3-dioxolane-2-one and 4,5-difluoro-1,3-dioxolane-2-one. Among others, preferably 4-fluoro-1,3-dioxolane-2-one (FEC) or propylene carbonate (PC) is used since it acts to suppress the degradation of other mixed solvents during high voltage charge/discharge, in a manner similar to ethylene carbonate (EC).
Also, a concentration of the high oxidation potential solvents in the solvent of electrolytic solution is not less than 5 vol % and not more than 60 vol %. If the concentration of the high oxidation potential solvent in the solvent of the electrolytic solution is at least 5 vol %, the degradation of the electrolytic solution is suppressed even in a cell having a high operating voltage. If the concentration is not more than 60 vol %, an increase in viscosity of the electrolytic solution is suppressed, and the electrolytic solution has liquidity to sufficiently immerse the positive electrode and the negative electrode in the electrolytic solution.
In addition, when the electrolytic solution contains a low-viscosity solvent, an increase in viscosity of the electrolytic solution is suppressed, and the electrolytic solution may have ion conductivity. The low-viscosity solvents include one or two compounds selected from dimethyl carbonate and fluorinated chain-type ethers.
As the fluorinated chain-type ethers, those of 2˜8 carbon atoms are preferably used. If the number of carbon atoms is not more than 8, viscosity increase of the electrolytic solution may be suppressed. Fluorinated chain-type ethers in which 30 atom % to 95 atom % of hydrogen atoms in alkyl groups are substituted with fluorine atoms are preferred. If fluorine substitution is at least 30 atom %, sufficient oxidation resistance is obtained. Also, if fluorine substitution is not more than 95 atom %, sufficient reduction resistance is obtained, and the reaction with the negative electrode may be suppressed. Specific examples of fluorinated chain-type ethers may include 1,1,2,2-tetrafluoroethyl-2,2,3,3-tetrafluoropropylether, 2,2,3,3,3-pentafluoropropyl-1,1,2,2-tetrafluoroethylether, 1,1,2,3,3,3-hexafluoropropylethylether, 2,2,3,4,4,4-hexafluorobutyldifluoromethylether, 1,1-difluoropropyl-2-fluoropropylether, 1,1,3-trifluoropropyl-2-fluoropropylether, 1,1,5-trifluoropentyl-1,1,2,2-tetrafluoroethylether or the like. Among others, 1,1,2,2-tetrafluoroethyl-2,2,3,3-tetrafluoropropylether, 2,2,3,3,3-pentafluoropropyl-1,1,2,2-tetrdfluoroethylether, 2,2,3,4,4,4-hexafluorobutyldifluoromethylether, 1,1-difluoropropyl-2-fluoropropylether or 1,1,3-trifluoropropyl-2-fluoropropylether are preferably used since they have low reactivity in the positive electrode and the negative electrode.
A content of the low-viscosity solvents in the solvent of the electrolytic solution is preferably not less than 5 vol % and not more than 80 vol %, and more preferably not less than 10 vol % and not more than 60 vol %. If the concentration of the low-viscosity solvents in the solvent of the electrolytic solution is at least 5 vol %, the electrolytic solution may have low viscosity required to immerse the electrodes therein and good ion conductivity.
Furthermore, the solvent of the electrolytic solution comprises preferably ethylene carbonate (EC). Since ethylene carbonate has high oxidation resistance and low reactivity with graphite, it is suitable for a cell using the positive electrode operating at a high voltage and the graphite negative electrode. Ethylene carbonate forms a film (Solid Electrolyte Interface: SEI) on the surface of the graphite negative electrode during primary charge. This film acts to suppress the subsequent reaction of the graphite and the electrolytic solution. Similar to ethylene carbonate, 4-fluoro-1,3-dioxolane-2-one (FEC) or propylene carbonate (PC) indicated above may also function to suppress the degradation of other mixed solvents by forming a film onto the surface of the negative electrode, and they are collectively referred to as “film-forming solvents”.
To form a film onto the surface of the negative electrode by a film-forming solvent and suppress the degradation of other solvents, a concentration of the film-forming solvent in the solvent of the electrolytic solution is preferable between 10 and 60 vol %, and more preferably not less than 20 vol % and not more than 60 vol %. If the concentration of the film-forming solvent in the solvent of the electrolytic solution is at least 10 vol %, SEI is formed to suppress gas generation during repetitive charge and discharge. If the concentration is not more than 60 vol %, an adverse effect on operation of a cell due to solidification of EC having a high melting point (37° C.) within the cell when the cell is used at a low temperature may be suppressed.
As ratios of mixed solvents in the solvent of the electrolytic solution, the ratios of the film-forming solvents 10˜60 vol %, the high oxidation potential solvents excluding FEC 5˜60 vol %, and the low-viscosity solvents 10˜80 vol % are preferred, and the ratios of the film-forming solvents 20˜60 vol %, the high oxidation potential solvents excluding FEC 5˜40 vol %, and the low-viscosity solvents 20˜60 vol % are more preferred. The sum of these ratios should be 100 vol %.
Also, the electrolytic solution may further contain solvents other than solvents indicated above (it is also referred to as “other solvents”) as long as they do not adversely affect solvents indicated above. Specific examples may include chain-type carbonates such as ethylmethyl carbonate, diethyl carbonate, dipropyl carbonate, fluorinated ethylmethyl carbonate, fluorinated dimethyl carbonate, or fluorinated diethyl carbonate; or carboxylic esters such as ethyl acetate, methyl propionate, ethyl formate, ethyl propionate, methyl butyric acid, ethyl butyric acid, methyl acetate, methyl formate or fluorinated derivatives thereof. Carboxylic esters having low viscosity may be used instead of chain-type carbonates or fluorinated ethers. Among others, preferably ethyl propionate or methyl acetate is used in terms of voltage resistance and boiling point. Also, examples may include γ-lactones such as γ-butyrolactone; chain-type ethers such as 1,2-ethoxyethane (DEE) or ethoxymethoxyethane (EME); cyclic ethers such as tetrahydrofuran or 2-methyltetrahydrofuran; or aprotic organic solvents such as dimethylsulfoxide, 1,3-dioxolane, formamide, acetoamide, dimethylformamide, dioxolane, acetonitrile, propylnitrile, nitromethane, ethylmonoglyme, trimethoxymethane, dioxolane derivatives, sulforane, methylsulforane, 1,3-dimethyl-2-imidazolidinone, 3-methyl-2-oxazolidinone, propylene carbonate derivatives, tetrahydrofuran derivatives, ethylethers, 1,3-propanesultone, anisole, N-methylpyrrolidone or others fluorinated compounds. They may be used alone or as any combination of two or more species.
A content of other solvents in the solvent of the electrolytic solution is preferably 0˜30 vol %, and more preferably 0˜20 vol %.
As an electrolyte that is contained in the electrolytic solution, lithium salts are preferably used. Specific examples of lithium salts may include LiPF6, LiAsF6, LiAlCl4, LiClO4, LiBF4, LiSbF6, LiCF3SO3, LiC4F9CO3, LiC(CF3SO2)3, LiN(CF3SO2)2, LiN(C2F5SO2)2, LiB10Cl10, lower aliphatic lithium carboxylate, chloroborane lithium, lithium tetraphenylborate, LiBr, LiI, LiSCN, LiCl, imides, boron fluorides or the like.
Moreover, ion conductive polymers may be used as the electrolyte. For example, polyethers such as polyethyleneoxide or polypropyleneoxide, polyolefins such as polyethylene or polypropylene, polyvinylidene fluoride, polytetrafluoroethylene, polyvinyl fluoride, polyvinyl chloride, polyvinylidene chloride, polymethyl metacrylate, polymethyl acrylate, polyvinyl alcohol, polymetacrylonitrile, polyvinyl acetate, polyvinylpyrrolidone, polycarbonate, polyethylene terephthalate, polyhexamethylene adipamide, polycaprolactame, polyurethane, polyethyleneimine, polybutadiene, polystyrene, or polyisoprene, derivatives thereof or copolymers of one or two or more of monomers constituting these polymers may be used. They may be used alone or as any combination of two or more species.
Inorganic solid electrolytic substances, any combinations of inorganic solid electrolytic substances and ion conductive polymers, inorganic solid powers bonded with organic binders, or the like may also be used.
They may be used alone or as any combination of two or more species.
A concentration of the electrolyte in the electrolytic solution is preferably not less than 0.01 mol/L and not more than 3 mol/L, and more preferably not less than 0.5 mol/L and not more than 1.5 mol/L. If the concentration of the electrolyte is within the ranges indicated above, cells having improved stability, increased reliability, and lowered environmental effect may be obtained.
Any separator may be used as long as it suppresses a contact of the positive electrode with the negative electrode, allows penetration of charge carriers, and has durability in the electrolytic solution. Specific materials suitable for the separator may include polyolefin, for example polypropylene or polyethylene based microporous membranes, celluloses, polyethylene terephthalate, polyimide, polyfluorovinylidene or the like. They may be used as a form such as porous film, fabric or nonwoven fabric.
Preferably, the cover body should have strength to stably hold the positive electrode, the negative electrode, the separator and the electrolytic solution, is electrochemically stable to these components, and has liquid-tightness. As specific examples, stainless steel, nickel-plated iron, aluminum, titanium, or alloys thereof or those plating, metal laminate resin or the like may be used. As resins suitable for the metal laminate resin, polyethylene, polypropylene, polyethylene terephthalate or the like may be used. They may be used as a structure of a single layer or two or more layers.
In a lithium secondary cell having configurations as described above, primary charge capacity is 140˜155 mAh/g with respect to about 148 mAh/g that is a theoretical value when all lithium ions are emitted. Also, primary discharge capacity is 120˜135 mAh/g, which corresponds to about 90% of the charge capacity. This lithium secondary cell has high energy density, suppresses the degradation of the electrolyte during subsequent repetitive charge and discharge to maintain high energy density, and has excellent cycle property.
A form of the lithium secondary cell may have any of cylindrical, flat winding rectangular, stacked rectangular, coin, flat winding laminate or stacked laminate forms.
As an example of the lithium secondary cell as indicated above, a coin-type secondary cell is shown in
Hereinafter, the lithium secondary cell according to the present invention will be described in detail.
A positive electrode active substance was prepared as follows. Ingredients MnO2, NiO and Li2CO3 were weighed so that a desired metal composition ratio was obtained. These ingredients were grinded and mixed. After mixing, the resulting power was fired at a firing temperature of 500˜1000° C. for 8 h to obtain LiNi0.5Mn1.5O4. The specific surface area of the resulting positive electrode active substance was 0.1˜2.0 m2/g.
A mixture for positive electrode was prepared by mixing the resulting positive electrode active substance, 5 wt % polyfluorovinylidene as a binding agent and 5 wt % carbon black as an electroconductive agent and the mixture is dispersed in N-methyl-2-pyrrolidone to obtain slurry. The slurry was uniformly coated onto one surface of an aluminum current collector having 20 μm thickness. A thickness of coated layer was adjusted such that primary charge capacity per unit area was 2.5 mAh/cm2. After drying, compression molding by a roll press was performed to fabricate a positive electrode.
As a negative electrode active substance, graphite coating by low-crystallinity carbon was used. The negative electrode active substance was dispersed in a solution of PVDF in N-methylpyrrolidone to obtain slurry. A weight ratio of the negative electrode active substance to a binding agent was 90/10. The slurry was uniformly coated onto a Cu current collector having 10 μm thickness. A thickness of coated layer was adjusted such that primary charge capacity was 3.0 mAh/cm2. After drying, compression molding by a roll press was performed to fabricate a negative electrode.
An electrolytic solution was prepared by mixing LiPF6 as an electrolyte at 1 mol/L concentration in a mix-solvent in which ethylene carbonate (EC), dimethyl carbonate (DMC), propylene carbonate (PC), butylene carbonate (BC), 4-fluoro-1,3-dioxolane-2-one (FEC) and 4,5-difluoro-1,3-dioxolane-2-one (FEC2) were mixed at a volume ratio indicated in Table 1.
A microporous polypropylene film having 25 μm thickness was used as a separator. A positive electrode and a negative electrode that are cut into 3 cm×1.5 cm respectively, with a tab connected to each end, were disposed opposite each other with the separator intervened. The resulting structure was disposed within a laminate cover body. An electrolytic solution was filled within the cover body, an end of each tab was drawn outwardly from the cover body, and the laminate of the cover body was sealed to obtain the coin-type secondary cell shown in
The resulting coin-type lithium secondary cell was charged at a constant current and voltage at 20° C., and subsequently was discharged at a constant current to measure discharge capacity. The discharge capacity was about 8 mAh. The charge and discharge were performed under the following conditions.
Then, this cell was subjected to repetitive cycles of charge at a constant current and voltage and discharge at a constant current at 20° C. and 45° C. After 50 cycles, discharge capacity was measured. The charge and discharge were performed under the following conditions.
In said Table, abbreviations represent the following compounds. The same is true of other tables.
EC: ethylene carbonate
DMC: dimethyl carbonate
PC: propylene carbonate
FEC: 4-fluoro-1,3-dioxolane-2-one
FEC2: 4,5-difluoro-1,3-dioxolane-2-one
BC: butylene carbonate
As can be seen from above, in cases of Examples using surface-treated graphite and high oxidation potential solvents as well as low-viscosity solvents, the lowering of capacity was suppressed after charge/discharge cycles, while in cases of Comparative Examples 1˜5 using graphite and Comparative Examples 6 and 7 using surface-treated graphite but not using high oxidation potential solvents, capacity was lowered after charge/discharge cycles.
Nine graphite materials were used as a negative electrode active substance. Surface crystallinity of these graphite materials was determined by Laser Raman scattering. A ratio (ID/IG) of the intensity of peak in D band (around 1360 cm−1) (ID) to the intensity of peak in G band (around 1600 cm−1) (IG), which was obtained by Raman Analysis, was calculated. The results are shown in Table 2.
Further, inner crystallinity of these negative electrode active substances was determined by X-ray diffraction. A layer spacing in 002 face d002 of graphite were measured.
Cells were fabricated and subjected to charge/discharge using the same method as Example 1 except for using these negative electrode active substances, LiNi0.5Mn1.5O4 as a positive electrode active substance, and EC/DMC/PC=50/40/10 (by volume) as a solvent of an electrolytic solution. The results are shown in Table 2.
As can be seen from above, in cases of Examples 4˜9 using graphite of which surface is coated by low-crystallinity carbon, the lowering of capacity was suppressed after charge/discharge cycles, while in cases of Comparative Examples 8 and 9 using graphite of which surface is not coated by low-crystallinity carbon and Comparative Example 10 using carbon material having amorphous surface, capacity was lowered after charge/discharge cycles.
Cells were fabricated and subjected to charge/discharge using the same method as Example 1 except for using solvents of electrolytic solution listed in Table 3, and Negative electrode material 8 indicated in Table 2 as the negative electrode active substance. The results are shown in Table 3.
In said Table, F-EPE represents 1,1,2,2-tetrafluoroethyl-2,2,3,3-tetrafluoropropylether.
In cases of Examples 10˜26 using low-viscosity solvents and high-oxidation-potential solvents, the lowering of capacity was suppressed after charge/discharge cycles, while in cases of Comparative Examples 6 and 7 that do not use low-viscosity solvents and Comparative Example 11 that does not use high-oxidation-potential solvents, capacity was lowered after charge/discharge cycles.
Cells were fabricated and subjected to charge/discharge using the same method as Example 1 except for using solvents of electrolytic solution listed in Table 4, 0.75 mol/L LiPF6 as the electrolyte, and Negative electrode material 8 indicated in said Table 2 as the negative electrode active substance. The results are shown in Table 4.
In said Table, abbreviations represent the following compounds.
FE1: 2,2,3,3,3-pentafluoropropyl-1,1,2,2-tetrafluoroethylether
FE2: 1,1,2,3,3,3-hexafluoropropylethylether
FE3: 2,2,3,4,4,4-hexafluorobutyldifluoromethylether
FE4: 1,1-difluoropropyl-2-fluoropropylether
FE5: 1,1,3-trifluoropropyl-2-fluoropropylether
FE6: 1,1,5-trifluoropentyl-1,1,2,2-tetrafluoroethylether
Electrolytic solution containing fluorinated chain-type ethers and PC or FEC exhibited good life property. As indicated in Comparative Example 12, in case of electrolytic solution containing EC and fluorinated chain-type ethers but not containing PC or FEC, capacity was lowered after cycles.
Positive electrode active substance were prepared using the same method as Example 1 except for weighing ingredients MnO2, NiO, Fe2O3, TiO2, B2O3, CoO, Li2CO3, MgO, Al2O3 and LiF as metal composition ratios indicated in Table 5. The specific surface areas of the resulting positive electrode active substances were 0.1˜2.0 m2/g.
Cells were fabricated and subjected to charge/discharge using the same method as Example 1 except for using positive electrode active substances listed in Table 5, Negative electrode material 8 indicated in said Table 2 as the negative electrode active substance, and EC/DMC/PC=50/40/10 (by volume) as the solvent of electrolytic solution. The results are shown in Table 5.
All of positive electrode materials operating at 4.5V or higher exhibited good cycle property.
Cells were fabricated and subjected to charge/discharge using the same method as Example 1 except for using positive electrode active substances listed in Table 6, Negative electrode material 8 indicated in Table 2 as the negative electrode active substance, EC/PC/F-EPE=10/30/50/10 (by volume) as the solvent of electrolytic solution, 0.75 mol/L LiPF6 as the electrolyte. The results are shown in Table 6.
The lithium secondary cell according to the present invention is fabricated by using the positive electrode comprising the lithium-manganese oxide complex represented by the formula (1) that operates at a high voltage of 4.5 V or more with respect to metallic lithium, the graphite coating by low-crystallinity carbon and the electrolytic solution containing the high oxidation potential solvent and the low-viscosity solvent (ethylene carbonate), and consequently the cell suppresses the lowering of capacity after charge/discharge cycles at a high temperature, and has high operating voltage, high energy density and long cell life under any environment.
This application incorporates the full disclosure of JP Patent Application No. 2011-089193 filed Apr. 13, 2011 herein by reference.
The present invention is applicable to all industrial fields that require power supply and industrial fields that, relate to transmission, storage and supply of electrical energy. Specifically, the present invention is applicable to power supply for mobile apparatuses such as mobile phone, notebook computer or the like.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2011-089193 | Apr 2011 | JP | national |
| Filing Document | Filing Date | Country | Kind | 371c Date |
|---|---|---|---|---|
| PCT/JP2012/060157 | 4/13/2012 | WO | 00 | 10/3/2013 |
