WO2002007239A1 - Non-aqueous electrolyte secondary cell - Google Patents
Non-aqueous electrolyte secondary cell Download PDFInfo
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- WO2002007239A1 WO2002007239A1 PCT/JP2001/006189 JP0106189W WO0207239A1 WO 2002007239 A1 WO2002007239 A1 WO 2002007239A1 JP 0106189 W JP0106189 W JP 0106189W WO 0207239 A1 WO0207239 A1 WO 0207239A1
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M4/00—Electrodes
- H01M4/02—Electrodes composed of, or comprising, active material
- H01M4/13—Electrodes for accumulators with non-aqueous electrolyte, e.g. for lithium-accumulators; Processes of manufacture thereof
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M4/00—Electrodes
- H01M4/02—Electrodes composed of, or comprising, active material
- H01M4/36—Selection of substances as active materials, active masses, active liquids
- H01M4/38—Selection of substances as active materials, active masses, active liquids of elements or alloys
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M10/00—Secondary cells; Manufacture thereof
- H01M10/05—Accumulators with non-aqueous electrolyte
- H01M10/052—Li-accumulators
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M4/00—Electrodes
- H01M4/02—Electrodes composed of, or comprising, active material
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M4/00—Electrodes
- H01M4/02—Electrodes composed of, or comprising, active material
- H01M4/36—Selection of substances as active materials, active masses, active liquids
- H01M4/38—Selection of substances as active materials, active masses, active liquids of elements or alloys
- H01M4/40—Alloys based on alkali metals
- H01M4/405—Alloys based on lithium
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
- Y02E60/10—Energy storage using batteries
Definitions
- the present invention relates to a non-aqueous electrolyte secondary battery. More specifically, the present invention relates to a non-aqueous electrolyte secondary battery having an improved negative electrode, high capacity, long life, and excellent high-rate discharge characteristics.
- the positive electrode of the non-aqueous electrolyte secondary battery has Li Mn 2 ⁇ 4 , Li Co 2 ,
- L i N i ⁇ 2, V 2 0 5, C r 2 0 5, M n 0 2, T i S 2, M o chalcogen compound such as S 2 can be used. These have a layered or tunnel structure through which lithium ions can enter and exit.
- metallic lithium can be used for the negative electrode of the nonaqueous electrolyte secondary battery.
- a battery with a high voltage and a high energy density can be realized.
- lithium metal when lithium metal is used, lithium dendrites precipitate on the surface of the lithium metal during charging, which lowers the charge / discharge efficiency or causes the dendrites to contact the positive electrode and cause an internal short circuit. . Therefore, in recent years, graphite-based carbon materials, which have a smaller capacity than metal lithium but can reversibly store and release lithium, have been used for the negative electrode. And lithium ion secondary batteries with excellent cycle characteristics and safety have been put to practical use.
- the practical capacity of carbon materials is as small as 35 OmAhZg, and the theoretical density of carbon materials is as low as 2.2 gZcc. Therefore, it is desired to use alloy particles that give a higher capacity negative electrode as the negative electrode material.
- alloys are generally associated with the introduction and desorption of lithium ions. It is pulverized by repeated expansion and contraction. The pulverized alloy loses contact with other alloy particles and conductive agent in the negative electrode, and lowers the conductivity of the negative electrode. That is, the finely divided alloy becomes an apparently inactive active material, and the capacity of the battery is reduced.
- Japanese Patent Application Laid-Open No. 11-88654 proposes that a phase capable of occluding lithium and a phase not occluding lithium coexist in one particle of an alloy as a negative electrode material.
- the phase that does not occlude lithium relaxes the expansion stress of the phase that occludes lithium, so that pulverization due to particle expansion is suppressed.
- Japanese Patent Application Laid-Open No. Hei 11-866853 proposes that two or more lithium absorbing phases coexist in one particle of an alloy as a negative electrode material. Although the particles expand, the expansion stress is different in each phase. By reducing the difference in the expansion coefficient between the two phases, the pulverization of the particles is suppressed. Each phase exists as small crystal grains in the particles. It is considered that stress is dispersed at the interface between crystal grains during lithium occlusion.
- the expansion coefficients of the phases differ greatly. As a result, non-uniform stress is generated in the particles, and strong stress is partially generated. A phase that does not occlude lithium cannot relieve this stress sufficiently. For this reason, it is thought that the particles eventually become fine and are released from the conduction network. In addition, the high-rate discharge characteristics of the battery are not sufficient because the phase that does not occlude lithium prevents the transfer of lithium ions.
- Ido et al. Have proposed a high-capacity and long-life negative electrode containing tin oxide (Sci ence, 276, 5317, 1395-1397 (1997)). However, it is necessary to reduce the divalent or tetravalent tin in the tin oxide to the zero-valent metal state during the first charging process. Therefore, the irreversible capacity of the battery increases, and the amount of lithium not involved in the charge / discharge cycle increases. Therefore, only low capacity batteries can be obtained.
- a battery using a negative electrode made of a conventional alloy or oxide has a problem that the cycle characteristics are easily deteriorated and the capacity is easily reduced. Disclosure of the invention
- An object of the present invention is to provide a non-aqueous electrolyte secondary battery having a high capacity, a long cycle life, and excellent high-rate discharge characteristics.
- the present invention provides a non-aqueous electrolyte secondary battery comprising a positive electrode capable of inserting and extracting lithium ions, a negative electrode capable of inserting and extracting lithium ions, and a non-aqueous electrolyte containing a lithium salt, wherein the negative electrode comprises: It is composed of alloy particles containing at least two members selected from the group consisting of a metal element and a metalloid element, and at least one member selected from oxygen and nitrogen, wherein the alloy particles electrochemically occlude lithium ions.
- a phase that can be released and electrochemically occludes lithium ions A phase B having ionic ion permeability, wherein the sum of the oxygen content Wao and the nitrogen content Wan in the A phase is less than 0.5% by weight, and the oxygen content Wbo and the nitrogen content Wbn in the B phase And a non-aqueous electrolyte secondary battery having a total of 1.0% by weight or more.
- Si or Sb can be used as the metalloid element.
- the A phase preferably contains at least one selected from the group consisting of Sn, Si, A and Ga, In, Pb, Sb, and Bi.
- the B phase preferably contains at least one selected from the group consisting of Ti, Zr and rare earth elements.
- the A phase is preferably surrounded by the B phase.
- Oxygen content Wao and nitrogen content W in the A phase and oxygen content Wbo and nitrogen content Wbn in the B phase are ((Wbo + Wbn) / (Wao +
- the oxygen content Wo and the nitrogen content Wn in the alloy particles are 0 ⁇ Wo ⁇ 10% by weight, 0 ⁇ Wn ⁇ 10% by weight, and 0.5% by weight ⁇ Wo + Wn ⁇ 10% by weight. Preferably, it is satisfied.
- the alloy particles may further include at least one selected from the group consisting of fluorine, sulfur, and phosphorus.
- the sum of at least one content Wf selected from the group consisting of fluorine, sulfur and phosphorus, oxygen content Wo, and nitrogen content Wn is 0.5 to 1 It is preferably 0% by weight. Further, Wf is preferably 0.5 to 1% by weight.
- FIG. 1 is a longitudinal sectional view of a test cell for evaluating the capacity characteristics of the alloy particles according to the present invention.
- FIG. 2 is a longitudinal sectional view of a cylindrical battery including the alloy particles according to the present invention.
- the present invention suppresses micronization accompanying expansion and contraction of a negative electrode material composed of alloy particles by the action of a B phase having lithium ion conductivity or lithium ion permeability containing at least one selected from oxygen and nitrogen. Things. If the B phase has lithium ion conductivity, the B phase is considered to have at least lithium ion permeability.
- the A phase includes at least one element selected from the group consisting of Sn, Si, Al, Ga, In, Pb, Sb, and Bi (hereinafter, referred to as a group A element). Is preferred. Group A elements are elements that easily form an alloy with lithium electrochemically. In the case of a lithium secondary battery using a negative electrode containing a Group A element, a large amount of lithium is absorbed and a high capacity can be obtained.
- the content of the group A element in the phase A is 5 Omo 1% or more.
- the B phase preferably contains at least one element selected from the group consisting of Ti, Zr, and a rare earth element (hereinafter, referred to as a group B element).
- a group B element a rare earth element
- La and Ce can be used as the rare earth element.
- Group B elements hardly react with lithium, but have high reactivity with oxygen and with nitrogen. Therefore, when the group A element and the group B element coexist in the presence of oxygen and nitrogen, the oxidation reaction and the nitridation reaction of the group B element occur preferentially, and the oxidation reaction and the nitridation reaction of the group A element are suppressed. If the above-mentioned reaction occurs in a state where the group A element and the group B element are forming or melting an intermetallic compound, the group A element and the group B element are in a state of being sufficiently finely dispersed. However, a low crystalline or amorphous B phase composed of fine crystal grains is formed.
- the content of group B elements in the alloy particles is preferably 5 to 70% by weight from the viewpoint of securing capacity. Further, it is desirable that the content be 5 to 30% by weight in terms of securing capacity, cycle life, and high-rate discharge characteristics.
- Group A elements also react with oxygen and nitrogen, but their reactivity is much lower than group B elements. Therefore, the amount of lithium ions absorbed and released by the phase A does not decrease.
- phase B does not contain group B elements, oxygen and nitrogen will react not only with phase B but also with phase A in the presence of oxygen and nitrogen. As a result, a large amount of oxides and nitrides are formed in the A phase, the amount of lithium absorbed and released is reduced, and the capacity is reduced.
- the A phase is preferably surrounded by the B phase.
- the alloy particles have such a structure, the stress generated by the expansion and contraction of the A phase is efficiently dispersed, and the effect of suppressing fine powder is enhanced.
- Oxygen content Wao and nitrogen content W in the A phase and oxygen content Wbo and nitrogen content Wbn in the B phase are ((Wbo + Wbn) / (Wao +
- Wan It is preferable to satisfy> 4.
- 4 ⁇ ⁇ (Wbo + Wbn) / (Wao + Wan) ⁇ the irreversible capacity at the time of the first charge increases because the content of oxygen and nitrogen in the A phase increases.
- the oxygen content Wo and the nitrogen content Wn in the alloy particles are 0 ⁇ Wo ⁇ 10% by weight and 0 ⁇ Wn ⁇ 10% by weight in terms of a balance between the discharge capacity, life characteristics, and high-rate discharge characteristics. And 0.5% by weight ⁇ Wo + Wn ⁇ 10% by weight is desirable. If Wo + Wn is less than 0.5% by weight, the fine powder of the present invention The effect of suppressing and improving the efficiency discharge characteristics is reduced. On the other hand, if Wo + Wn exceeds 10% by weight, the irreversible capacity at the time of the first charge increases, and the discharge capacity decreases. Also, if the alloy particles contain excessive amounts of oxygen and nitrogen, the active material density will decrease and the volume energy density will decrease. Therefore, 1 weight
- the alloy particles may include at least one selected from the group consisting of fluorine, sulfur, and phosphorus, in addition to at least one selected from oxygen and nitrogen.
- Fluorine, sulfur and phosphorus are selectively introduced into phase B over phase A.
- fluorine, sulfur or phosphorus is introduced into phase B, fluoride, sulfide or phosphide is introduced into phase B. Generate.
- lithium ion conductivity and lithium ion permeability are further improved, and excellent high-rate discharge characteristics can be obtained.
- the total content of the content of at least one selected from the group consisting of fluorine, sulfur, and phosphorus, the content of oxygen, and the content of nitrogen in the alloy particles must be determined. It is preferably 0.5 to 10% by weight, more preferably 1 to 5% by weight.
- At least one selected from the group consisting of fluorine, sulfur and phosphorus contained in the alloy particles It is preferable that 70% by weight or more of the total amount of oxygen and nitrogen is contained in the B phase.
- Oxygen and nitrogen can be introduced into the alloy while controlling the amounts thereof using a gas atomizing method, a water atomizing method, a mechanical alloying method, or the like. At least one selected from the group consisting of fluorine, sulfur and phosphorus can likewise be incorporated into the alloy.
- the test cell was used to evaluate the capacity characteristics of the alloy particles.
- the test cell shown in FIG. 1 was manufactured.
- a negative electrode mixture was prepared by mixing 7.5 g of negative electrode alloy particles, 2 g of graphite powder as a conductive agent, and 0.5 g of polyethylene powder as a binder. 0.1 g of this mixture was pressure-molded to a diameter of 17.5 mm to obtain a test electrode 1. Test electrode 1 was placed in case 2. Next, a microporous polypropylene separator was placed on the test electrode 1.
- the opening of the case 2 was sealed with a sealing plate 6 having a metal gasket 5 having a diameter of 17.5 mm stuck to the inner surface thereof and a polypropylene gasket 5 arranged around the periphery to complete the test cell.
- Cylindrical batteries were used to evaluate high rate discharge characteristics and cycle life.
- the cylindrical battery shown in FIG. 2 was manufactured.
- L i M n>. 8 Co which is a positive electrode active material. . 2 0 4, and L i 2 C_ ⁇ 3 and M n 3 ⁇ 4 and C o CO 3 were mixed at a predetermined molar ratio, was synthesized by heating in 9 0 0 ° C.
- the positive electrode active material was classified to 100 mesh or less.
- An aqueous dispersion containing 100 g of the above positive electrode active material, 100 g of carbon powder as a conductive agent, and 8 g of polytetrafluoroethylene as a binder And an appropriate amount of pure water were added and mixed well to obtain a paste.
- the obtained paste was applied to an aluminum core material, dried and rolled to obtain a positive electrode 11.
- a positive electrode lead 14 made of aluminum was attached to the positive electrode core material by ultrasonic welding.
- alloy particles, graphite powder as a conductive agent, and styrene butadiene rubber as a binder were mixed at a weight ratio of 70:20:10, and an appropriate amount of water was added to the obtained mixture.
- the obtained paste was applied to a copper core material and dried at 140 ° C. to obtain a negative electrode 12.
- a negative electrode lead 15 made of copper was attached to the negative electrode core material by ultrasonic welding.
- the positive electrode and the negative electrode were spirally wound via a strip-shaped porous polypropylene separator 13 wider than both the electrode plates, to form an electrode plate group.
- the electrode group was provided with insulating plates 16 and 17 made of polypropylene on the upper and lower portions, respectively, and inserted into the battery case 18.
- a mixed solution of ethylene carbonate and dimethoxyethane in which L i C 1 O 4 was dissolved and having a volume ratio of 1: 1 was injected into a battery case 18 as a non-aqueous electrolyte.
- the opening of the battery case 18 was sealed with a sealing plate 19 having a positive electrode terminal 20 to complete a cylindrical battery.
- the test cell was charged at a constant current of 0.5 mA / cm 2 until the terminal voltage became 0 V (a reaction in which lithium ions were inserted into the alloy particles).
- discharge reaction to release lithium ions from alloy particles
- the discharge capacity was obtained. The ratio of the discharge capacity to the charge capacity
- R disc / c was determined in percentage.
- the low percentage value R disc / c indicates that many irreversible reactions occur during the first charge, that is, electrochemical Means that the irreversible capacity is large.
- a cylindrical battery is charged at a constant current of 0.2 C (5 hour rate) at 20 ° C until the battery voltage reaches 4.2 V, and then a constant voltage charge is performed at 4.2 V Was. Then, the first discharge was performed at a constant current of 0.2 C until the battery voltage reached 3.0 V.
- the battery was charged under the same conditions as before, and discharged at a constant current of 2 C (0.5 hour rate) until the battery voltage reached 3.0 V.
- the value obtained by dividing the discharge capacity at the second 2 C current by the discharge capacity at the first 0.2 C discharge and multiplying by 100 is the high rate discharge ratio (R 2 C / Q.2 C) And asked. High rate discharge ratio R 2C /.
- the bulk single raw material was mixed at a predetermined ratio along the raw material composition (T i 2 Sn) shown in Table 1.
- the obtained mixture was produced in an arc melting furnace.
- Injection nozzle diameter used in Gasua Bok Mize method is l mm phi, gas injection pressure was l OO kgf Zc m 2.
- Argon gas containing 1% oxygen (Example 1), oxygen % Argon gas (Example 2), argon gas containing 5% oxygen (Example 3), nitrogen gas containing 1% oxygen (Example 4), nitrogen gas containing 3% oxygen (Example 5) or Nitrogen gas containing 5% oxygen (Example 6) was used.
- the alloy particles obtained by the gas atomizing method were passed through a 45-micron mesh sieve to obtain a powder having an average particle size of 28 / m. ⁇
- the oxygen content Wao and the nitrogen content Wan in the A phase, and the oxygen content Wbo and the nitrogen content Wbn in the B phase were determined by a transmission electron microscope (TEM) and an electron energy loss analysis (EELS). That is, the oxygen content and the nitrogen content were calculated by observing several points on the cross section of the particle by TEM, analyzing by EELS, and converting the obtained element ratio into a weight ratio. Table 1 shows the results.
- TEM transmission electron microscope
- EELS electron energy loss analysis
- the oxygen content Wo in the alloy particles was determined by an infrared absorption method according to JISZ2613.
- the nitrogen content Wn in the alloy particles was determined by a thermal conductivity method in accordance with JISG122. Table 1 shows the results.
- Spherical alloy particles were obtained in the same manner as in Example 1 except that the type of injection gas in the gas atomizing method was changed as shown in Table 1.
- the granular single raw material was prepared according to the raw material composition shown in Table 1: FeSi (Comparative Example 4), FeSn2 (Comparative Example 5) or NiAl (Comparative Example 6) at a predetermined ratio.
- the alloy was obtained in the same manner as in Example 1 except that the alloys were mixed at different ratios. From the obtained alloy, spherical alloy particles were obtained under the same conditions as in Example 1 by using a gas atomizing method.
- Example 1 shows the results.
- Table 2 shows the results.
- the B phase does not contain Ti, Zr, or a rare earth element. Therefore, the oxygen content and the nitrogen content in the phase A are large as shown in Table 1, respectively, and the ratio of the discharge capacity to the initial charge capacity ( Rdisc / C ) is also greatly reduced.
- Granular elemental material the raw material shown in Table 3 Composition: along the C u Z r S i 2, were mixed in a ratio of Jo Tokoro.
- the obtained mixture was produced in an arc melting furnace.
- spherical alloy particles were obtained from the obtained alloy by using a gas atomizing method.
- composition Composition (wt%) (wt%) (wt%)
- the oxygen content Wo and the nitrogen content Wn contained in the entire alloy particles are less than 0 Wo ⁇ 10% by weight, 0 ⁇ Wn ⁇ 10% by weight, 0% 5% by weight ⁇ Wo + Wn ⁇ 10% by weight. Further, the batteries of Examples 7 to 12 all have high capacity, excellent high-rate discharge characteristics, and long life. Examples 13 to 14
- the raw material composition shown in Table 3 is: Granular single raw material: NiLaGa or
- Alloy particles were obtained from the obtained alloy using a water atomizing method. Water atomization was performed in a nitrogen atmosphere. Oxygen and nitrogen introduced into the alloy by the water atomization method are supplied from oxygen and nitrogen dissolved in water, and from oxygen generated by decomposition of water at the time of collision between water and molten metal. In the water atomizing method, the alloy is rapidly cooled and pulverized by squirting water with a jet pressure of 800 kgf / cm 2 onto the molten alloy. The obtained alloy particles were passed through a 45-micron mesh sieve to obtain a powder having an average particle diameter of 20 / im.
- Example 3 shows the results.
- the test cells and cylindrical batteries manufactured using the alloy particles were evaluated in the same manner as in Example 1.
- Table 4 shows the results.
- E PMA analysis of the particle cross-section revealed that an oxide film with an average thickness of about 18 nm was formed on the surface of the particles synthesized by the water atomization method.
- Table 3 shows that much more oxygen and nitrogen are introduced into phase B than from phase A.
- the alloy particles of Examples 13 to 14 all are contained in the entire alloy particles.
- the oxygen content Wo and the nitrogen content Wn satisfy 0 ⁇ Wo ⁇ 10% by weight, 0 ⁇ Wn ⁇ 10% by weight, 0.5% by weight ⁇ Wo + Wn ⁇ 10% by weight.
- the batteries of Examples 13 to 14 all have high capacity, excellent high-rate discharge characteristics, and long life.
- the B phase containing a large amount of oxygen and nitrogen was found to be in a low crystalline or amorphous state by TEM observation and electron diffraction analysis. Many grain boundaries were formed in the B phase, partly forming fine oxides and nitrides.
- the conduction path of lithium ions in the particles increased, and good lithium ion conductivity was developed, and the high-rate discharge characteristics of the battery were also improved.
- the B-phase is also suitable for absorbing the stress caused by the expansion and contraction of the A-phase, thus improving the cycle life of the battery. Introducing oxygen into the B phase can provide some effect of stress relaxation, but it is thought that the effect of stress relaxation will be greatly improved if nitrogen is further introduced into the B phase.
- Examples 15 to 17 predetermined additives having a particle size of 45 m or less shown in Table 5 were put into a pot mill at a ratio shown in Table 5 with respect to the total of raw materials and additives. .
- the granular L i F was used as an additive.
- the total amount of raw materials to be put into the pot mill was 15 g including additives.
- An argon gas containing 3% oxygen was sealed in the pot mill.
- the pot mill was operated at a constant rotation of 60 rpm for 10 days. As a result, alloy particles having an average particle size of about 0.8 m were obtained.
- Example 5 shows the results.
- the test cells and cylindrical batteries manufactured using the alloy particles were evaluated in the same manner as in Example 1.
- Table 6 shows the results.
- Example 10 The obtained alloy particles were analyzed in the same manner as in Example 1. Table 5 shows the results. The test cells and cylindrical batteries manufactured using the alloy particles were evaluated in the same manner as in Example 1. Table 6 shows the results. Comparative Example 10-; L 4
- Example 5 shows the results. Further, the test cells and the cylindrical batteries manufactured using the alloy particles were evaluated in the same manner as in Example 1. Table 6 shows the results.
- Comparative Examples 10 to 14 were inadequate because the alloy particles contained almost no oxygen or nitrogen, the grain boundaries in the particles were small, and the expansion stress was large. This is considered to be because it is difficult to alleviate the problem. Comparative Examples 15 to 19
- Example 5 shows the results.
- the test cells and cylindrical batteries manufactured using the alloy particles were evaluated in the same manner as in Example 1.
- Table 6 shows the results.
- Examples 15 to 24 contain more oxygen and nitrogen in the B phase.
- the batteries of Examples 15 to 24 are excellent in high-rate discharge characteristics and life characteristics.
- the batteries of Comparative Examples 10 to 14 containing alloy particles synthesized in a high-purity Ar gas atmosphere have insufficient life characteristics and high-rate discharge characteristics.
- the batteries of Comparative Examples 15 to 19 containing alloy particles synthesized in an air atmosphere may have a large irreversible capacity because the oxygen content and the nitrogen content in the A phase of the alloy particles are too large. Understand.
- the battery using the alloy particles according to the examples of the present invention for the negative electrode has higher capacity, cycle characteristics and higher rate discharge characteristics than the battery of the comparative example. It was excellent.
- the B phase contained 70% by weight or more of the total amount of oxygen and nitrogen.
- alloy particles that provide high capacity, excellent high rate discharge characteristics, and a long life battery have an oxygen content "o" and a nitrogen content Wn of 0 ⁇ Wo ⁇ 10% by weight, Wn ⁇ 10% by weight and 0.5% by weight ⁇ Wo + Wn ⁇ 10% by weight were satisfied.
- the positive electrode L i Mn o D. 2 Rei_4 a has been described about the case of using, and L i Mn 2 ⁇ 4, L i C O_ ⁇ 2, L i N i O 2 Needless to say, the same effect can be obtained even if used.
Description
Claims
Priority Applications (2)
Application Number | Priority Date | Filing Date | Title |
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US10/088,398 US6761998B2 (en) | 2000-07-19 | 2001-07-17 | Non-aqueous electrolyte secondary cell |
EP01948051.6A EP1302994B1 (en) | 2000-07-19 | 2001-07-17 | Non-aqueous electrolyte secondary cell |
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JP2000218528A JP4608743B2 (ja) | 2000-07-19 | 2000-07-19 | 非水電解質二次電池 |
JP2000-218528 | 2000-07-19 |
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PCT/JP2001/006189 WO2002007239A1 (en) | 2000-07-19 | 2001-07-17 | Non-aqueous electrolyte secondary cell |
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US (1) | US6761998B2 (ja) |
EP (1) | EP1302994B1 (ja) |
JP (1) | JP4608743B2 (ja) |
WO (1) | WO2002007239A1 (ja) |
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CN100382362C (zh) * | 2003-03-26 | 2008-04-16 | 佳能株式会社 | 用于锂二次电池的电极材料和具有该电极材料的电极结构 |
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JP4366222B2 (ja) * | 2003-03-26 | 2009-11-18 | キヤノン株式会社 | リチウム二次電池用の電極材料、該電極材料を有する電極構造体、該電極構造体を有する二次電池 |
US20060083986A1 (en) * | 2004-03-16 | 2006-04-20 | Wen Li | Battery with tin-based negative electrode materials |
JP4802570B2 (ja) | 2005-06-24 | 2011-10-26 | パナソニック株式会社 | リチウムイオン二次電池用負極、その製造方法、およびそれを用いたリチウムイオン二次電池 |
JP5072323B2 (ja) * | 2005-11-17 | 2012-11-14 | パナソニック株式会社 | 非水電解質二次電池、および非水電解質二次電池用負極材料の製造方法 |
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JP2008300234A (ja) * | 2007-05-31 | 2008-12-11 | Fuji Heavy Ind Ltd | 電極材料の製造方法、及び電極材料、並びに非水系リチウムイオン二次電池 |
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Also Published As
Publication number | Publication date |
---|---|
US6761998B2 (en) | 2004-07-13 |
US20030068558A1 (en) | 2003-04-10 |
EP1302994A1 (en) | 2003-04-16 |
EP1302994B1 (en) | 2018-05-16 |
JP4608743B2 (ja) | 2011-01-12 |
JP2002042805A (ja) | 2002-02-08 |
EP1302994A4 (en) | 2006-01-25 |
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