Patent Application
20130084499
1. Field of the Invention
The present invention relates to a non-aqueous electrolyte secondary battery. Particularly, the present invention relates to a non-aqueous electrolyte secondary battery comprising lithium vanadium phosphate and lithium nickel composite oxide as positive electrode active material.
2. Related Art
Non-aqueous electrolyte secondary batteries such as lithium ion secondary batteries are currently used as power sources of electric appliance and the like, and furthermore, as power sources of electronic automobiles (such as EV (electric vehicle) and HEV (hybrid electric vehicle), etc.). In addition, non-aqueous electrolyte secondary batteries such as lithium ion secondary batteries require further improvement in more characteristics, such as improvement in energy density (realization of high capacity), improvement in power density (realization of high power) and improvement in cycle characteristics (improvement in cycle lifespan), high safety and the like.
Recently, most of lithium ion secondary batteries used for small-sized electric appliances and the like use lithium composite oxide such as LiCoO2 as positive electrode active materials and realize electric storage devices with high capacity and long lifespan. However, these positive-electrode active materials have problems that, at a high temperature and a high electric potential when an abnormality occurs, the positive-electrode active materials excessively react with an electrolyte to generate a heat while releasing oxygen. In the worst case, they may ignite.
Recently, olivine-type Fe(LiMnPO4), olivine-type Mn(LiMnPO4) having similar crystalline structures with the olivine-type Fe, and the like are considered as positive electrode active materials that exhibit superior thermal stability even in high temperature and high electric potential states. Such positive-electrode active materials have practically used, for example, in electrical tools. However, LiFePO4 has an operation voltage of 3.3 to 3.4V with respect to Li/Li+, which is lower than the operation voltage of positive electrode active materials used for general-application batteries, thus being insufficient in terms of energy density or power density. In addition, LiMnPO4 has a operation voltage of 4.1V with respect to Li/Li+ and a theoretical capacity of 160 mAh/g, thus realizing batteries with a high energy density, but having disadvantages of high inherent resistance of materials and melting of Mn at high temperatures.
Accordingly, batteries satisfying high capacity, high power, long lifespan and superior safety cannot be realized, even if olivine-type materials are used.
Meanwhile, recently, NASICON-type lithium vanadium phosphate, i.e., Li3V2(PO4)3 attracts much attention as a similar positive electrode active material with superior thermal stability (for example, Patent Document 1: JP-A-2001-500665). Li3V2(PO4)3 has an operation voltage of 3.8V with respect to Li/Li+ and a large capacity of 130 to 195 mAh/g according to respective electric potential plateaus. Furthermore, electric conductivity can be improved and high power can be thus realized by coating conductive carbon on the surface of a positive electrode active material selected from olivine iron materials.
In conventional cases, in order to stabilize characteristics of batteries, secure reliability and safety, and realize high energy, taking into consideration power properties of positive and negative electrodes, it is designed such that relation of x and y satisfies 0.95<y/x<1, assuming that the first charge capacity of negative electrode per unit area is x (mAh/cm2) and the first charge capacity of positive electrode per unit area is y (mAh/cm2). However, in batteries with high power and high capacity, when short-circuit is caused by a sticking of conductive metal foreign materials or the like, a great amount of lithium ions are released from the negative electrode to the positive electrode for a short time. Non-aqueous secondary batteries comprising a positive electrode containing Li3V2(PO4)3 and lithium nickel composite oxide exhibit good lithium ion receiving property of the positive electrode, but disadvantageously exhibit low lithium ion donor property of the negative electrode, when short-circuit occurs. This low donor property causes considerable heating of negative electrode and abnormal heating or heating of cells. In the worst case, combustion occurs. When non-aqueous secondary batteries are mounted on mobile equipment such as vehicle equipment, the sticking of the conductive metal foreign materials may occur. Accordingly, abnormal heating or combustion of cells should be prevented.
One or more embodiments provide a high power and high capacity non-aqueous electrolyte secondary battery including a positive electrode containing lithium vanadium phosphate, wherein the non-aqueous electrolyte secondary battery has safety and good cycle properties in which an abnormal heating or combustion of cells does not occur even when short-circuit is caused by sticking of conductive metal foreign materials or the like.
Embodiments will be described in detail. The embodiments relate to a non-aqueous electrolyte secondary battery. Examples of the non-aqueous electrolyte secondary battery may be lithium ion secondary batteries. As described below, according to the embodiments, configurations of the non-aqueous electrolyte secondary battery are not particularly limited except for a positive electrode and a negative electrode, and conventional techniques may be suitably combined so long as effects of the invention are not impaired.
The non-aqueous electrolyte secondary battery according the embodiments includes a positive electrode including a positive electrode mixture layer containing positive electrode active materials. The positive electrode active materials includes NASICON-type lithium vanadium phosphate, i.e., Li3V2(PO4)3 and lithium nickel composite oxide.
Further, although the Li3V2(PO4)3 is explained as an exemplary embodiment of the NASICON-type lithium vanadium phosphate according to the embodiments, the NASICON-type lithium vanadium phosphate which can be expressed as LiXV2-y My (PO4), (in which M is one or more selected from a group formed by Fe, Co, Mn, Cu, Zn, Al, Sn, B, Ga, Cr, V, Ti, Mg, Ca, Sr, and Zr, and a relation of x, y and z satisfies 1≦x≦3, 0≦y<2, and 2≦z≦3) may be used as materials having effects similar to Li3V2(PO4)3.
According to the embodiments, the Li3V2(PO4)3 may be prepared by any method. For example, the Li3V2(PO4)3 may be prepared by a method including mixing a lithium source such as LiOH or LiOH.H2O, a vanadium source such as V2O5 or V2O3 and a phosphate source such as NH4H2PO4 or (NH4)2HPO4, followed by reacting and baking and the like. The Li3V2(PO4)3 may be usually in the form of a particle obtained by grinding the baked substance or the like.
Since an electrical conductivity of the Li3V2(PO4)3 is originally low, it is required to coat surfaces of the Li3V2(PO4)3 with conductive carbon. Thereby, the electrical conductivity of the Li3V2(PO4)3 can be improved. A coating amount of conductive carbon is preferably 0.1 to 20 mass % in terms of C atom.
The conductive carbon coating may be performed by a well-known method. For example, the conductive carbon coating can be formed on the surface of Li3V2(PO4)3 by mixing citric acid, ascorbic acid, polyethylene glycol, sucrose, methanol, propene, carbon black, Ketjen black or the like as a carbon coating material during reaction or baking in the production of Li3V2(PO4)3.
The particle sizes of the Li3V2(PO4)3 particles are not particularly limited and those having the desired particle size may be used. Since the particle size affects stability or density of the Li3V2(PO4)3, D50 in the particle size distribution of secondary particles of the Li3V2(PO4)3 is preferably 0.5 to 25 μm. When the D50 is lower than 0.5 μm, a contact area with the electrolytic solution increases and stability of the Li3V2(PO4)3 may be deteriorated. When the D50 exceeds 25 μm, power may be deteriorated due to deterioration in density. When D50 falls within the range, electric storage devices with superior stability and higher power can be obtained. In the particle size distribution of secondary particles of the Li3V2(PO4)3, the D50 is more preferably 1 to 10 μm, particularly preferably 3 to 5 μm. Furthermore, in the particle size distribution of secondary particles, the D50 is a value measured using a particle size distribution measuring apparatus based on a laser diffraction (light scattering) manner.
According to the embodiments, various lithium nickel composite oxides may be used. A content of Ni element in the lithium nickel composite oxide affects proton absorption property of the lithium nickel composite oxide. According to the embodiments, the Ni element is preferably present in an amount of 0.3 to 0.8 moles, and more preferably 0.5 to 0.8 moles with respect to one mole of lithium atom. When the content of the Ni element is excessively low, the inhibition effect of elution of vanadium from the Li3V2(PO4)3 may be insufficient. When the content is within this range, as the content of Ni element increases, the inhibition effect of elution of vanadium from Li3V2(PO4)3 is improved. Specifically, when the content of the Ni element is 0.5 or more, a capacity maintaining rate is remarkably improved due to the inhibition effect of elution of vanadium.
In addition, according to the embodiments, in the lithium nickel composite oxide, a metal element different from Ni, having an atomic number of 11 or higher may be substituted into the Ni site. The metal element different from Ni, having an atomic number of 11 or higher, is preferably selected from transition metal elements. The transition elements may have a plurality of oxidation numbers like Ni, thus using the oxidation and reduction range in the lithium nickel composite oxide and maintaining high capacity properties. The metal element different from Ni, having an atomic number of 11 or higher, is for example Co, Mn, Al or Mg, preferably Co or Mn.
According to the embodiments, the lithium nickel composite oxide may be a material expressed for example as LiXNi1-yM′yO2 (in which, “x” satisfies 0.85≦x≦1.2, “y” satisfies 0.2≦y≦0.7, and M′ is one or more selected from a group including Fe, Co, Mn, Cu, Zn, Al, Sn, B, Ga, Cr, V, Ti, Mg, Ca and Sr). It is preferable that “y” satisfies 0.2≦y≦0.5.
The lithium nickel composite oxide may be prepared by any method. For example, the lithium nickel composite oxide may be prepared by mixing a Ni-containing precursor synthesized by a solid phase reaction method, a co-precipitation method, a sol gel method or the like and a lithium compound at a desired stoichiometric ratio, followed by baking under an air atmosphere or the like.
The lithium nickel composite oxide may be usually in the form of a particle obtained by grinding the baked substance. The particle size thereof is not particularly limited and those having the desired particle size may be used. Since the particle size affects stability or density of lithium nickel composite oxide, an average particle size of particles is preferably 0.5 to 25 μm. When the average particle size is lower than 0.5 μm, a contact area with the electrolytic solution increases and stability of lithium nickel composite oxide may be deteriorated. When the average particle size exceeds 25 μm, power may be deteriorated due to deterioration in density. When the average particle size falls within the range, electric storage devices with superior stability and higher power can be obtained. The average particle size of particles of lithium nickel composite oxide is more preferably 1 to 25 μm, particularly preferably 5 to 20 μm. Furthermore, the average particle size of these particles is a value measured using a particle size distribution measuring apparatus based on a laser diffraction (light scattering) manner.
According to the embodiments, the positive electrode may be prepared by using well-known materials as far as the positive electrode active materials includes the carbon coated Li3V2(PO4)3 and lithium nickel composite oxide. For example, the positive electrode may be prepared by production processes as described in detail below.
A positive electrode mixture layer is formed by a process including applying a positive electrode slurry obtained by dispersing a mixture including the positive electrode active material, a binder and a conductive agent in a solvent onto a positive electrode collector and drying the applied substance. After drying, pressing may be performed. As a result, the positive electrode mixture layer is uniformly and firmly pressed on the collector. The positive electrode mixture layer preferably has a thickness of 10 to 200 μm, preferably 20 to 100 μm.
The binder used for formation of the positive electrode mixture layer is for example a fluorine-containing resin such as polyvinylidene fluoride, an acrylic binder, a rubber-based binder such as SBR, a thermoplastic resin such as polypropylene and polyethylene, carboxymethylcellulose or the like. The binder is preferably a fluorine-containing resin or a thermoplastic resin that is chemically and electrochemically stable to non-aqueous electrolytic solution used for electric storage devices of the embodiments, particularly preferably a fluorine-containing resin. Examples of the fluorine-containing resin include polyvinylidene fluoride as well as polytetrafluoroethylene, vinylidene fluoride-trifluoroethylene copolymers, ethylene-tetrafluoroethylene copolymers and propylene-tetrafluoroethylene copolymers and the like. The content of the binder is preferably 0.5 to 20% by mass with respect to the positive electrode active material.
The conductive agent used for formation of the positive electrode mixture layer is for example conductive carbon such as Ketjenblack, a metal such as copper, iron, silver, nickel, palladium, gold, platinum, indium or tungsten, or conductive metal oxide such as indium oxide and tin oxide. The content of conductive material is preferably 1 to 30 mass % with respect to the positive electrode active material.
The solvent used for the formation of the positive electrode mixture layer may be water, isopropyl alcohol, N-methylpyrrolidone, dimethylformamide or the like.
As far as a surface of the positive electrode collector that contacts the positive electrode mixture layer is a conductive base material having conductivity, the positive electrode collector may be any material. The positive electrode collector is, for example, a conductive base material made of a conductive material such as metal, conductive metal oxide or conductive carbon, or a non-conductive base material coated with a conductive material. The conductive material is preferably copper, gold, aluminum or an alloy thereof or conductive carbon. The positive electrode collector may be an expended metal, a punched metal, a foil, a net, a foamed material or the like of the material. In cases of porous materials, the shape or number of through holes is not particularly limited and may be suitably determined no long as the movement of lithium ions is not inhibited.
The content of lithium nickel composite oxide in the positive electrode active material is 5 to 95 mass %. When the content of lithium nickel composite oxide is excessively low, inhibition effects of elution of vanadium from Li3V2(PO4)3 are not sufficiently exerted and superior cycle properties cannot be obtained. In addition, high capacity cannot be obtained. On the other hand, when the content of lithium nickel composite oxide is excessively high, elution of vanadium from Li3V2(PO4)3 can be inhibited, but charge and discharge cycle properties of electric storage devices may be not sufficiently improved. The reason for this would be that low stability of lithium nickel composite oxide causes deterioration. Within this range, high capacity and superior cycle properties can be obtained.
According to the embodiments, the negative electrode includes carbon-based active material capable of intercalating and deintercalating lithium ions, for example lithium intercalation carbon material. A negative electrode slurry obtained by dispersing a mixture including the negative electrode active material and a binder in a solvent is applied to a negative electrode collector, followed by drying to form a negative electrode mixture layer. Furthermore, the binder, the solvent and the collector may be ones similar to those of the aforementioned positive electrode.
In addition, the lithium intercalation carbon material may be, for example, graphite, carbon-based materials such as non-graphitizable carbon, polyacene materials and the like. The polyacene material is for example insoluble and unmeltable PAS having a polyacene skeleton. Furthermore, these lithium intercalation carbon materials are substances that are capable of reversibly doping lithium ions. The negative electrode mixture layer generally has a thickness of 10 to 200 μm, preferably 20 to 100 μm.
Furthermore, according to the embodiments, the coating amounts of negative electrode and positive electrode mixture layers are designed such that relation of x and y is adjusted to 0.6≦y/x≦0.92, assuming that the first charge capacity of negative electrode per unit area is x (mAh/cm2), and the first charge capacity of positive electrode per unit area is y (mAh/cm2), in terms of capacity balance between positive and negative electrodes and energy density, while the relation is set at 0.95<y/x<1 in conventional cases. Here, the coating amount of negative electrode and x, and the coating of positive electrode and y are linearly related to each other, respectively. That is, as the coating amount is doubled, x or y is also doubled.
According to the embodiments, the non-aqueous electrolytic solution is not particularly limited and may be a well-known non-aqueous electrolytic solution. For example, an electrolytic solution obtained by dissolving a general lithium salt as an electrolyte in an organic solvent may be used in that it does not cause electrolysis even at a high voltage and lithium ions can be stably present.
Examples of the electrolyte include CF3SO3Li, C4F9SO8Li, (CF3SO2)2NLi, (CF3SO2)3CLi, LiBF4, LiPF6, LiClO4 and combinations thereof.
Examples of the organic solvent include propylene carbonate, ethylene carbonate, buthylene carbonate, dimethyl carbonate, diethyl carbonate, ethylmethyl carbonate, vinyl carbonate, trifluoromethyl propylene carbonate, 1,2-dimethoxyethane, 1,2-diethoxyethane, γ-butyrolactone, tetrahydrofuran, 1,3-dioxolane, 4-methyl-1,3-dioxolane, diethylether, sulfolan, methylsulfolan, acetonitrile, propionitrile and mixtures thereof.
A concentration of electrolyte in the non-aqueous electrolytic solution is preferably 0.1 to 5.0 mol/L, more preferably, 0.5 to 3.0 mol/L.
The non-aqueous electrolytic solution may be a liquid state, a solid electrolyte or a polymer gel electrolyte in which a plasticizer or polymer is incorporated.
According to the embodiments, the separator is not particularly limited and may be a well-known separator. For example, a porous material that exhibits durability to an electrolytic solution, a positive electrode active material and a negative electrode active material, has communication holes and has no electrical conductivity is preferably used. Examples of this porous material include woven fabrics, non-woven fabrics, synthetic resin microporous membranes, glass fibers and the like. The synthetic resin microporous membrane is preferably used and a microporous membrane made of polyolefin such as polyethylene or polypropylene is particularly preferably used, in terms of thickness, membrane strength and membrane resistance.
Hereinafter, as an exemplary embodiment of non-aqueous electrolyte secondary battery, an example of lithium ion secondary battery will be described with reference to the drawings.
The positive electrode 21 includes a positive electrode mixture layer 21a containing a positive electrode active material and a positive electrode collector 21b. The positive electrode mixture layer 21a is disposed on a surface of the positive electrode collector 21b at a side of the separator 23. The negative electrode 22 includes a negative electrode mixture layer 22a and a negative electrode collector 22b. The negative electrode mixture layer 22a is disposed on a surface of the negative electrode collector 22b at a side of the separator 23. The positive electrode 21, the negative electrode 22, and the separator 23 are mounted in an exterior container (not shown) and the exterior container is filled with a non-aqueous electrolytic solution. Examples of the container include battery cans, laminate films and the like. The positive electrode collector 21b and the negative electrode collector 22b are optionally connected to leads for connections of exterior terminals (not shown).
Then,
Furthermore, the lithium ion secondary battery 30 may be provided with a lithium electrode to allow lithium ions to be freely doped into a positive electrode and/or a negative electrode. In this case, movement of lithium ions is facilitated, and the positive electrode collector 31b or the negative electrode collector 32b is provided with through holes that extend in the lamination direction of the electrode unit 34.
In addition, the lithium ion secondary battery 30 has a structure in which negative electrodes are arranged in the uppermost and the lowermost parts and is not limited to the structure. The lithium ion secondary battery 30 may have a structure in which positive electrodes are arranged in the uppermost and the lowermost parts.
Hereinafter, examples will be described.
The following substances for the positive electrode mixture layer were mixed to obtain a positive electrode slurry.
First active material (Li3V2(PO4)3); 30 parts by mass
Second active material (LiNi0.8Co0.1Mn0.1O2); 60 parts by mass
Binder (polyvinylidene fluoride (PVdF)); 5 parts by mass
Conductive agent (carbon black); 5 parts by mass
Solvent (N-methyl2-pyrrolidone (NMP)); 100 parts by mass
The positive electrode slurry was applied to a positive electrode collector of an aluminum foil (thickness 30 μm), followed by drying to form a positive electrode mixture layer on the positive electrode collector. The coating amount (per one surface) of the positive electrode mixture layer was 14 mg/cm2. After formation of the positive electrode mixture layer, a coated region (region where the positive electrode mixture layer is formed) except an uncoated region with a size of 10×10 mm as a tab for lead connection was cut to a size of 50×50 mm. Li3V2(PO4)3 for the first active material used herein was coated with 1.4% by mass of carbon in terms of C atom.
The following substances for the negative electrode mixture layer were mixed to obtain a negative electrode slurry.
Active material (graphite); 95 parts by mass
Binder (PVdF); 5 parts by mass
Solvent (NMP); 150 parts by mass
The negative electrode slurry was applied to a negative electrode collector of an aluminum foil (thickness 10 μm), followed by drying to form a negative electrode mixture layer on the negative electrode collector. The coating amount (per one surface) of the negative electrode mixture layer was 7.2 mg/cm2. A relation of x and y was adjusted to y/x=0.9, assuming that the first charge capacity of negative electrode per unit area was x (mAh/cm2) and the first charge capacity of positive electrode per unit area was y (mAh/cm2). After formation of the negative electrode mixture layer, a coated region (region where the negative electrode mixture layer was formed) except an uncoated region with a size of 10×10 mm as a tab for lead connection was cut to a size of 52×52 mm.
A lithium ion secondary battery according to the embodiment shown in
The positive electrode leads and the negative electrode leads of batteries thus fabricated were connected to the corresponding terminals of a charge and discharge tester (manufactured by Asuka Electronics Co. Ltd.) and constant-voltage constant-current charged at a maximum voltage of 4.2V and a current rate of 2 C and constant-current discharged at a current rate 5 C up to 2.5V after charge. These processes were repeated 1000 cycles. An energy density (Wh/kg) was calculated from the capacity measured during the first discharge and a cycle capacity maintenance ratio (discharge capacity during 1000 cycles/discharge capacity during the first cycle×100) was calculated from the capacity after cycles. The capacity maintenance ratio was 92%. The measurement results are shown in Table 1.
The positive electrode leads and the negative electrode leads of batteries thus fabricated were connected to the corresponding terminals of a charge and discharge tester (manufactured by Asuka Electronics Co. Ltd.) and constant-voltage constant-current charged at a maximum voltage of 4.2V and a current rate of 5 C. An iron nail with a diameter of φ5 mm was prepared and a lithium ion secondary battery was put on a substrate made of a metal. The nail was pierced at a nail piercing rate of 15 mm/sec in the center of lithium ion secondary battery in the lamination direction of positive and negative electrodes and passed through an aluminum laminate. The aluminum laminate was observed 10 minutes after the nail was pierced, but abnormal heating and combustion of cells did not occur. The observation results are shown in Table 1. In Table 1, “GOOD” means that abnormal heating and combustion were not observed and “NG” means that abnormal heating and combustion occurred.
A battery was fabricated and tested in the same manner as in Example 1, except that the coating amount (per one surface) of the negative electrode mixture layer was changed into 10.6 mg/cm2 such that relation of x and y satisfied y/x=0.6, assuming that the first charge capacity of negative electrode per unit area was x (mAh/cm2) and the first charge capacity of positive electrode per unit area was y (mAh/cm2). The capacity maintenance ratio was 87% and abnormal heating and combustion did not occur in the safety test using nail piercing.
A battery was fabricated and tested in the same manner as in Example 1, except that the coating amount (per one surface) of the negative electrode mixture layer was changed into 7.6 mg/cm2 such that relation of x and y satisfied y/x=0.85, assuming that the first charge capacity of negative electrode per unit area was x (mAh/cm2) and the first charge capacity of positive electrode per unit area was y (mAh/cm2). The capacity maintenance ratio was 91% and abnormal heating and combustion did not occur in the safety test using nail piercing.
A battery was fabricated and tested in the same manner as in Example 1, except that the coating amount (per one surface) of the negative electrode mixture layer was changed into 6.8 mg/cm2 such that relation of x and y satisfied y/x=0.95, assuming that the first charge capacity of negative electrode per unit area was x (mAh/cm2) and the first charge capacity of positive electrode per unit area was y (mAh/cm2). The capacity maintenance ratio was 92% and abnormal heating and combustion did not occur in the safety test using nail piercing.
A battery was fabricated and tested in the same manner as in Example 1, except that the coating amount (per one surface) of the negative electrode mixture layer was changed into 11.7 mg/cm2 such that relation of x and y satisfied y/x=0.55, assuming that the first charge capacity of negative electrode per unit area was x (mAh/cm2) and the first charge capacity of positive electrode per unit area was y (mAh/cm2). The capacity maintenance ratio was 78% and abnormal heating and combustion did not occur in the safety test using nail piercing. The results of Examples 1 to 3 and Comparative Examples 1 and 2 are shown in Table 1.
A battery was fabricated and tested in the same manner as in Example 1, except that the coating amount (per one surface) of the negative electrode mixture layer was changed into 7.0 mg/cm2 such that relation of x and y satisfied y/x=0.92, assuming that the first charge capacity of negative electrode per unit area was x (mAh/cm2) and the first charge capacity of positive electrode per unit area was y (mAh/cm2). The capacity maintenance ratio was 90% and abnormal heating and combustion did not occur in the safety test using nail piercing.
A battery was fabricated and tested in the same manner as in Example 1, except that the second active material of the positive electrode mixture layer was changed to LiNi0.8CO0.1Al0.1O2, and the coating amount (per one surface) of the negative electrode mixture layer was changed into 7.3 mg/cm2 such that relation of x and y satisfied y/x=0.92, assuming that the first charge capacity of negative electrode per unit area was x (mAh/cm2) and the first charge capacity of positive electrode per unit area was y (mAh/cm2). The capacity maintenance ratio was 90% and abnormal heating and combustion did not occur in the safety test using nail piercing.
A battery was fabricated and tested in the same manner as in Example 1, except that the second active material of the positive electrode mixture layer was changed to LiNi0.6Co0.2Mn0.2O2, and the coating amount (per one surface) of the negative electrode mixture layer was changed into 6.1 mg/cm2 such that relation of x and y satisfied y/x=0.92, assuming that the first charge capacity of negative electrode per unit area was x (mAh/cm2) and the first charge capacity of positive electrode per unit area was y (mAh/cm2). The capacity maintenance ratio was 89% and abnormal heating and combustion did not occur in the safety test using nail piercing.
A battery was fabricated and tested in the same manner as in Example 1, except that the second active material of the positive electrode mixture layer was changed to LiNi0.5Co0.3Mn0.2O2, and the coating amount (per one surface) of the negative electrode mixture layer was changed into 6.1 mg/cm2 such that relation of x and y satisfied y/x=0.92, assuming that the first charge capacity of negative electrode per unit area was x (mAh/cm2) and the first charge capacity of positive electrode per unit area was y (mAh/cm2). The capacity maintenance ratio was 89% and abnormal heating and combustion did not occur in the safety test using nail piercing.
A battery was fabricated and tested in the same manner as in Example 1, except that the second active material of the positive electrode mixture layer was changed to LiNi0.6CO0.2Mn0.2O2, and the coating amount (per one surface) of the negative electrode mixture layer was changed into 5.9 mg/cm2 such that relation of x and y satisfied y/x=0.95, assuming that the first charge capacity of negative electrode per unit area was x (mAh/cm2) and the first charge capacity of positive electrode per unit area was y (mAh/cm2). The capacity maintenance ratio was 90% and abnormal heating and combustion occurred in the safety test using nail piercing.
A battery was fabricated and tested in the same manner as in Example 1, except that the second active material of the positive electrode mixture layer was changed to LiNi0.5CO0.3Mn0.2O2, and the coating amount (per one surface) of the negative electrode mixture layer was changed into 5.9 mg/cm2 such that relation of x and y satisfied y/x=0.95, assuming that the first charge capacity of negative electrode per unit area was x (mAh/cm2) and the first charge capacity of positive electrode per unit area was y (mAh/cm2). The capacity maintenance ratio was 90% and abnormal heating and combustion occurred in the safety test using nail piercing.
A battery was fabricated and tested in the same manner as in Example 1, except that the second active material of the positive electrode mixture layer was changed to LiNi0.6Co0.2Mn0.2O2, and the coating amount (per one surface) of the negative electrode mixture layer was changed into 10 mg/cm2 such that relation of x and y satisfied y/x=0.55, assuming that the first charge capacity of negative electrode per unit area was x (mAh/cm2) and the first charge capacity of positive electrode per unit area was y (mAh/cm2). The capacity maintenance ratio was 76% and abnormal heating and combustion does not occur in the safety test using nail piercing.
A battery was fabricated and tested in the same manner as in Example 1, except that the second active material of the positive electrode mixture layer was changed to LiNi0.5Co0.3Mn0.2O2, and the coating amount (per one surface) of the negative electrode mixture layer was changed into 10 mg/cm2 such that relation of x and y satisfied y/x=0.55, assuming that the first charge capacity of negative electrode per unit area was x (mAh/cm2) and the first charge capacity of positive electrode per unit area was y (mAh/cm2). The capacity maintenance ratio was 75% and abnormal heating and combustion does not occur in the safety test using nail piercing.
The results of Examples 4 to 7 and Comparative Examples 3 to 6 are shown in Tables 2 and 3.
As can be seen from the test results of Examples 1 to 7, when the value of y/x was adjusted within the range of 0.6 to 0.92, assuming that the first charge capacity of negative electrode per unit area was x (mAh/cm2) and the first charge capacity of positive electrode per unit area was y (mAh/cm2), the lithium deintercalation margin of negative electrode increased and good results could be obtained in safety test using nail piercing. When the value of y/x was lower than the lower limit, 0.6, good results could be obtained in the safety test using nail piercing, but good results could not be obtained in the current load test. The reason for this is thought that deintercalation margin of lithium ions on the negative electrode is excessively high, causing unbalance in charge capacity between the positive electrode and the negative electrode. In addition, it is thought that, when the value of y/x is higher than 0.92, in the safety test using nail piercing, deintercalation margin of lithium ions on the negative electrode is low, similar to conventional cases, causing abnormal heating of cells.
Furthermore, the present invention is not limited to the construction of aforementioned embodiments and Examples, but various modifications are possible within the scope of the subject matters of the invention.
In accordance with the embodiments, a non-aqueous electrolyte secondary battery may include a positive electrode active material including a carbon-coated lithium vanadium phosphate and a lithium nickel composite oxide, and a negative electrode active material including a carbon-based active material capable of intercalating and deintercalating lithium ions. When a first charge capacity of a negative electrode per unit area is “x” (mAh/cm2) and a first charge capacity of a positive electrode per unit area is “y” (mAh/cm2), a relation of “x” and “y” may satisfy 0.6≦y/x≦0.92.
The lithium vanadium phosphate may be expressed as LiXV2-yMy(PO4)z, in which M is one or more selected from a group formed by Fe, Co, Mn, Cu, Zn, Al, Sn, B. Ga, Cr, V, Ti, Mg, Ca, Sr, and Zr, and in which a relation of x, y and z satisfies 1≦x≦3, 0≦y<2, and 2≦z≦3. For example, the lithium vanadium phosphate may be Li3V2(PO4)3.
According to the embodiments, a positive electrode active material includes carbon-coated lithium vanadium phosphate and lithium nickel composite oxide, and a negative electrode active material comprises a carbon-based active material capable of intercalating and deintercalating lithium ions. Here, the lithium deintercalation margin of negative electrode is set at a higher level than conventional cases. Specifically, the lithium deintercalation margin of the negative electrode is adjusted to a high level such that the relation of x and y satisfies 0.6≦y/x≦0.92, assuming that the first charge capacity of negative electrode per unit area is x (mAh/cm2), and the first charge capacity of positive electrode per unit area is y (mAh/cm2).
Accordingly, a non-aqueous electrolyte secondary battery in which a donor property of lithium ions from the negative electrode is improved so that an abnormal heating or combustion of cells does not occur even when a short-circuit is caused by a sticking of conductive metal foreign materials or the like and a safety and superior cycle properties can be exhibited can be provided.
According to the embodiments, since the non-aqueous electrolyte secondary battery uses carbon-coated lithium vanadium phosphate and lithium nickel composite oxide as positive electrode active materials, high power and superior safety as well as high capacity, and good charge and discharge properties can be obtained by setting an amount of lithium nickel composite oxide in the positive electrode active material.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2011-216098 | Sep 2011 | JP | national |
| 2012-153335 | Jul 2012 | JP | national |
