Positive electrode active material for lithium ion secondary battery, positive electrode for lithium ion secondary battery, lithium ion secondary battery, electronic device, and vehicle

Abstract

A positive electrode active material for a lithium ion secondary battery has a rock salt type structure represented by General Formula:
Li.sub.xTi.sub.2x-1Mn.sub.2-3xO (0.50<x<0.67)(1)
and has an average particle size of 0.5 m or less.

Claims

1. A positive electrode active material for a lithium ion secondary battery having a rock salt type structure represented by General Formula:
Li.sub.xTi.sub.2x-1Mn.sub.2-3xO (0.55x<0.63)(1) and having an average particle size of 0.5 m or less.

2. The positive electrode active material for a lithium ion secondary battery according to claim 1, wherein, in charge compensation according to movement of lithium ions during charging and discharging, the contribution of oxide ions to oxidation reduction is equal to or greater than the contribution of transition metal ions contained in a solid solution to oxidation reduction.

3. A positive electrode for a lithium ion secondary battery comprising the positive electrode active material for a lithium ion secondary battery according to claim 1, a conductive material, and a binder.

4. A lithium ion secondary battery comprising the positive electrode for a lithium ion secondary battery according to claim 3, a negative electrode, and a nonaqueous electrolyte.

5. The lithium ion secondary battery according to claim 4, wherein an initial charging capacity is 260 mAh/g or more.

6. An electronic device comprising the lithium ion secondary battery according to claim 5 as a drive power source.

7. A vehicle comprising the lithium ion secondary battery according to claim 5 as a drive power source.

8. A positive electrode active material for a lithium ion secondary battery having a rock salt type structure represented by General Formula:
Li.sub.xTi.sub.yMn.sub.(3-y-4x)/2Nb.sub.(2x-y-1)/2O (0.55x<0.63, 0<y<(1x))(2) and having an average particle size of 0.5 m or less.

9. The positive electrode active material for a lithium ion secondary battery according to claim 8, wherein, in charge compensation according to movement of lithium ions during charging and discharging, the contribution of oxide ions to oxidation reduction is equal to or greater than the contribution of transition metal ions contained in a solid solution to oxidation reduction.

10. A positive electrode for a lithium ion secondary battery comprising the positive electrode active material for a lithium ion secondary battery according to claim 8, a conductive material, and a binder.

11. A lithium ion secondary battery comprising the positive electrode for a lithium ion secondary battery according to claim 10, a negative electrode, and a nonaqueous electrolyte.

12. The lithium ion secondary battery according to claim 11, wherein an initial charging capacity is 260 mAh/g or more.

13. An electronic device comprising the lithium ion secondary battery according to claim 12 as a drive power source.

14. A vehicle comprising the lithium ion secondary battery according to claim 12 as a drive power source.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

(1) FIG. 1 is a block diagram of main functions of a mobile phone including a lithium ion secondary battery according to the present embodiment as a drive power source.

(2) FIG. 2 is a block diagram of a drive system of an electric vehicle including the lithium ion secondary battery according to the present embodiment as a drive power source.

(3) FIG. 3 is a microscopic image of a substance after a positive electrode active material for a lithium ion secondary battery is ground by ball milling when a positive electrode for the lithium ion secondary battery is produced.

(4) FIG. 4 shows X-ray diffraction images before and after ball milling is performed on a powder of a composite oxide obtained in Example 1-1.

(5) FIG. 5 shows charging and discharging characteristics of an electrochemical cell obtained using a composite oxide Li.sub.0.6Ti.sub.0.2Mn.sub.0.2O (x=0.6) of Example 1-1 as a positive electrode active material.

(6) FIG. 6 shows evaluation results of a capacity retention characteristic of a discharging capacity of an electrochemical cell using a composite oxide Li.sub.0.6Ti.sub.0.2Mn.sub.0.2O (x=0.6) of Example 1-1 as a positive electrode active material.

(7) FIG. 7 shows charging and discharging characteristics of an electrochemical cell measured under conditions of Example 1-2 using a composite oxide Li.sub.0.6Ti.sub.0.2Mn.sub.0.2O (x=0.6) as a positive electrode active material.

(8) FIG. 8 shows charging and discharging characteristics of an electrochemical cell measured under conditions of Example 1-3 using a composite oxide Li.sub.0.6Ti.sub.0.2Mn.sub.0.2O (x=0.6) as a positive electrode active material.

(9) FIG. 9 shows evaluation results of a capacity retention characteristic of a discharging capacity of an electrochemical cell under conditions of Example 1-3 using a composite oxide Li.sub.0.6Ti.sub.0.2Mn.sub.0.2O (x=0.6) as a positive electrode active material.

(10) FIG. 10 shows X-ray diffraction images before and after ball milling is performed on a powder of a composite oxide obtained in Example 2.

(11) FIG. 11 shows charging and discharging characteristics of an electrochemical cell obtained using a composite oxide Li.sub.0.55Ti.sub.0.1Mn.sub.0.35O (x=0.55) of Example 2 as a positive electrode active material.

(12) FIG. 12 shows X-ray diffraction images before and after ball milling is performed on a powder of a composite oxide obtained in Example 3.

(13) FIG. 13 shows charging and discharging characteristics of an electrochemical cell obtained using a composite oxide Li.sub.0.62Ti.sub.0.245Mn.sub.0.135O (x=0.62) of Example 3 as a positive electrode active material.

(14) FIG. 14 shows X-ray diffraction images before and after ball milling is performed on a powder of a composite oxide obtained in Reference Example 1.

(15) FIG. 15 shows charging and discharging characteristics of an electrochemical cell obtained using a composite oxide Li.sub.0.625Ti.sub.0.1Nb.sub.0.075Mn.sub.0.2O (x=0.625, y=0.1) in Reference Example 1 as a positive electrode active material.

DETAILED DESCRIPTION OF THE INVENTION

(16) Forms for implementing a positive electrode active material for a lithium ion secondary battery, a positive electrode for a lithium ion secondary battery, a lithium ion secondary battery, an electronic device and a vehicle according to the present embodiment will be described below.

(17) <Positive Electrode Active Material for Lithium Ion Secondary Battery>

(18) A positive electrode active material for a lithium secondary battery according to one aspect of the present invention is composed of a solid solution of Li.sub.2TiO.sub.3 and LiMnO.sub.2 and has a rock salt type structure. As another aspect, a positive electrode active material for a lithium secondary battery may be composed of a solid solution of Li.sub.2TiO.sub.3, LiMnO.sub.2 and Li.sub.3NbO.sub.4. The common point between these positive electrode active materials for a lithium secondary battery is that both solid solutions include Li.sub.2TiO.sub.3 and LiMnO.sub.2.

(19) The positive electrode active material for a lithium ion secondary battery may contain other materials within a range in which effects of the present invention are obtained.

(20) When the positive electrode active material for a lithium secondary battery is composed of a solid solution of Li.sub.2TiO.sub.3 and LiMnO.sub.2, it is represented by General Formula
Li.sub.xTi.sub.2x-1Mn.sub.2-3xO (0.50<x<0.67)(1).

(21) The solid solution of Li.sub.2TiO.sub.3 and LiMnO.sub.2 can be represented by the following formula by adjusting a coefficient of oxygen.
xLi.sub.2/3Ti.sub.1/3O.(1x)Li.sub.1/2Mn.sub.1/2O (0.50<x<0.67)

(22) When this is changed and represented by MeO (Me: metal) having a rock salt type structure, the above General Formula (1) is obtained.

(23) In addition, when the positive electrode active material for a lithium secondary battery is composed of a solid solution of Li.sub.2TiO.sub.3, LiMnO.sub.2 and Li.sub.3NbO.sub.4, it is represented by General Formula:
Li.sub.xTi.sub.yMn.sub.(3-y-4x)/2Nb.sub.(2x-y-1)/2O (0<x<1, 0<y<(1x))(2).

(24) The solid solution of Li.sub.2TiO.sub.3, LiMnO.sub.2 and Li.sub.3NbO.sub.4 can be represented by the following formula by adjusting a coefficient of oxygen.
aLi.sub.2/3Ti.sub.1/3O.bLi.sub.1/2Mn.sub.1/2O.(1ab)Li.sub.3/4Nb.sub.1/4O (0<a<1, 0<b<1)

(25) When this is changed and represented by MeO (Me: metal) having a rock salt type structure, the above General Formula: Li.sub.(9-a-3b)/12Ti.sub.a/3Mn.sub.b/2Nb.sub.(1-a-b)/4O is obtained.

(26) In addition, when x=(9a3b)/12, and y=a/3 are set in order for the obtained general formula to be combined with General Formula (1), General Formula (2) is obtained.

(27) In the positive electrode active material for a lithium secondary battery according to one aspect of the present invention, in charge compensation according to movement of lithium ions during charging and discharging, the contribution of oxide ions to oxidation reduction is equal to or greater than the contribution of transition metal ions contained in a solid solution to oxidation reduction.

(28) That is, in the positive electrode active material for a lithium ion secondary battery according to one aspect of the present invention, in charge compensation according to movement of lithium ions during charging and discharging, the contribution of oxide ions to oxidation reduction is great.

(29) Here, the contribution of oxide ions to oxidation reduction or the contribution of transition metal ions to oxidation reduction refers to the contribution of oxide ions or transition metal ions to oxidation reduction in charge compensation according to movement of lithium ions during charging and discharging when oxidation reduction reactions reversibly and stably occur.

(30) As an example, it refers to the contribution of oxide ions or transition metal ions to oxidation reduction in charging and discharging when oxidation reduction reactions reversibly occur over at least 30 cycles or more.

(31) For example, when the positive electrode active material for a lithium ion secondary battery is composed of a solid solution of Li.sub.2TiO.sub.3 and LiMnO.sub.2, in charge compensation according to movement of lithium ions during charging and discharging, there are a contribution according to a change in the valence of Mn.sup.3+/Mn.sup.4+ and a contribution according to a change in the valence of oxide ions of O.sub.2.sup.2/2O.sup.2.

(32) For example, when the positive electrode active material for a lithium ion secondary battery is Li.sub.0.6Ti.sub.0.2Mn.sub.0.2O (formula weight: 81.453), if the contribution according to a change in the valence of Mn.sup.3+/Mn.sup.4+ is the main contribution, a theoretical capacity is 131.6 mAh/g. On the other hand, when a theoretical capacity is obtained from a movement amount of lithium ions during charging and discharging, the theoretical capacity is 394.9 mAh/g.

(33) The movement amount of lithium ions during charging and discharging is a sum of the contribution according to a change in the valence of Mn.sup.3+/Mn.sup.4+ and the contribution according to a change in the valence of O.sub.2.sup.2/2O.sup.2. That is, the charging and discharging capacities can be increased using not only the contribution according to a change in the valence of Mn.sup.3+/Mn.sup.4+ but also the contribution according to a change in the valence of oxide ions of O.sub.2.sup.2/2O.sup.2.

(34) The contribution of oxide ions to oxidation reduction and the contribution of transition metal ions to oxidation reduction can be examined by measuring changes in the valence of transition metal ions and oxide ions during a charging and discharging cycle. The changes in the valence of transition metal ions and oxide ions can be examined through, for example, soft X-ray absorption spectroscopy (XAS), X-ray photoelectron spectroscopy (XPS), X-ray absorption fine structure analysis (XAFS), or electron energy loss spectroscopy (EELS).

(35) For example, when the positive electrode active material for a lithium ion secondary battery is composed of a solid solution of Li.sub.2TiO.sub.3 and LiMnO.sub.2, changes in the valence of manganese ions Mn.sup.3+/Mn.sup.4+ and oxide ions of O.sub.2.sup.2/2O.sup.2 can be measured through soft X-ray absorption spectroscopy or the like. During charging, the contribution of manganese ions to oxidation reduction reactions can be examined according to a change of manganese ions from Mn.sup.3+ to Mn.sup.4+ (generation of Mn.sup.4+), and the contribution of oxide ions to oxidation reduction reactions can be examined according to a change from 2O.sup.2 to O.sub.2.sup.2 (generation of O.sub.2.sup.2 and analogues thereof). On the other hand, during discharging also, the contribution of manganese ions to oxidation reduction reactions can be confirmed according to a change of manganese ions from Mn.sup.4+ to Mn.sup.3+ (generation of Mn.sup.3+) and the contribution of oxide ions to oxidation reduction reactions can be confirmed according to a change from O.sub.2.sup.2 to 2O.sup.2 (generation of O.sup.2).

(36) In addition, the contribution of oxide ions to oxidation reduction or the contribution of transition metal ions to oxidation reduction can be theoretically predicted from the composition.

(37) For example, it is known that Li.sub.2TiO.sub.3 is electrochemically inactive. Therefore, for example, when a compositional proportion of Mn in General Formula:
Li.sub.xTi.sub.2x-1Mn.sub.2-3xO (0.50<x<0.67)(1)
is larger than a compositional proportion of Ti, the contribution of transition metal ions to oxidation reduction is predicted to be great, and when a compositional proportion of Mn and a compositional proportion of Ti are equal, the contribution of oxide ions to oxidation reduction is predicted to be great.

(38) In General Formulae (1) and (2), x is 0.50<x<0.67. When x is a composition in this range, it is easy to maintain a rock salt type structure. In addition, x is preferably 0.52x<0.65. When x is a composition in this range, it is easier to maintain a rock salt type structure. In addition, x is more preferably 0.55x<0.63. When x is a composition in this range, large charging and discharging capacities are remarkably obtained.

(39) The positive electrode active material for a lithium ion secondary battery according to the present embodiment also contains a slightly deviated composite oxide due to inevitable loss of Li, Ti, Mn, Nb or O.

(40) <Method of Producing Positive Electrode Active Material for Lithium Ion Secondary Battery>

(41) In a method of producing a positive electrode active material for a lithium ion secondary battery according to one aspect of the present invention, salts or oxides of lithium, titanium, manganese, and niobium are prepared and the positive electrode active material can be obtained by a solid-phase method according to compositional proportions.

(42) In addition, the method is not limited to the solid-phase method, but a coprecipitation method, an evaporation drying method, a spray dry method or the like can be used.

(43) The salts or oxides of lithium, titanium, manganese, and niobium may be separately prepared or may be prepared as a composite compound. For example, a lithium titanium composite oxide containing a lithium compound and a titanium compound, a lithium manganese composite oxide containing a lithium compound and a manganese compound, a lithium niobium composite oxide containing a lithium compound and a niobium compound, or the like may be prepared in advance.

(44) As the lithium compound, lithium hydroxide, lithium citrate, lithium oxalate, lithium phosphate, lithium carbonate, or the like can be used, and these may be used alone or two or more thereof may be used in a mixture.

(45) As the titanium compound, metal titanium, titanium oxide, titanium hydroxide, titanium nitrate, titanium chloride, or the like can be used, and these may be used alone or two or more thereof may be used in a mixture. In consideration of stability, titanium oxide (TiO.sub.2) or the like is preferably used.

(46) As the manganese compound, metal manganese, manganese oxide, manganese hydroxide, manganese nitrate, manganese carbonate, manganese chloride, manganese iodide, or manganese sulfate can be used, and these may be used alone or two or more thereof may be used in a mixture. Manganese carbonate is preferable.

(47) As the niobium compound, metal niobium, niobium oxide, niobium oxalate, niobium chloride, niobium carbide, or lithium niobate can be used, and these may be used alone or two or more thereof may be used in a mixture. In consideration of stability and easy availability, niobium pentoxide (Nb.sub.2O.sub.5) is preferable.

(48) When synthesizing is performed by the solid-phase method, the salts or oxides of lithium, titanium, manganese, and niobium are adjusted so that a target active material has desired compositional proportions and the adjusted mixture is calcined, and thereby a positive electrode active material for a lithium ion secondary battery is obtained.

(49) Regarding the amount of a lithium raw material, since a part of the lithium raw material is eliminated during calcination, the lithium raw material is preferably contained in an excessive amount of about 1 to 5%. In addition, a calcination temperature depends on a type of a lithium salt to be used, and is preferably 500 C. or higher, and more preferably 800 C. or higher in order to increase the crystallinity of a positive electrode active material for a lithium ion secondary battery to be generated. When the crystallinity of a positive electrode active material for a lithium ion secondary battery to be generated is higher, charging and discharging characteristics are improved.

(50) <Positive Electrode for a Lithium Ion Secondary Battery>

(51) A positive electrode for a lithium ion secondary battery according to one aspect of the present invention includes the positive electrode active material for a lithium ion secondary battery, a conductive material, and a binder.

(52) The positive electrode for a lithium ion secondary battery according to one aspect of the present invention may include the positive electrode active material for a lithium ion secondary battery alone as a positive electrode active material or may additionally include one or more known positive electrode active materials for a lithium ion secondary battery.

(53) In addition, when the positive electrode for a lithium ion secondary battery according to one aspect of the present invention is produced, the positive electrode active material for a lithium ion secondary battery is preferably ground by ball milling or the like.

(54) The average particle size of the ground positive electrode active material for a lithium ion secondary battery is preferably 0.5 m or less. FIG. 3 is a microscopic image of a substance after the positive electrode active material for a lithium ion secondary battery is ground by ball milling when the positive electrode for a lithium ion secondary battery is produced. Here, the average particle size is an average value of particle sizes of 20 arbitrary particles in the optical microscope image. The particle size of the positive electrode active material for a lithium ion secondary battery before grinding is performed by ball milling is 2 to 4 m, and the maximum particle size of the ground substance is about 1 m.

(55) The average particle size of the positive electrode active material for a lithium ion secondary battery using oxidation reduction reactions of a transition metal such as a general layered oxide is 1 to 5 m. The average particle size is a factor that greatly contributes to charging and discharging characteristics. It was newly found through study that, when the average particle size is set to 0.5 m or less and uniform compositing with a carbon material is performed, charge compensation according to oxide ions becomes active and initial charging and discharging characteristics of the lithium ion secondary battery become 260 mAh/g or more. In addition, it was newly found that an actually measured value of initial charging and discharging characteristics with respect to a Li-based theoretical capacity can be 70% or more.

(56) In addition, when ball milling or the like is performed, for example, a conductive material such as carbon is preferably mixed with the positive electrode active material for a lithium ion secondary battery. When a grinding process is performed by ball milling or the like, the conductive material uniformly adheres to a surface of the ground positive electrode active material for a lithium ion secondary battery. A complexing agent in which a conductive material such as carbon uniformly adheres to a surface of a positive electrode active material for a lithium ion secondary battery has excellent charging and discharging characteristics because charge compensation according to oxide ions occurs. In addition, in order to avoid unnecessary reactions, the grinding process is preferably performed in an inert gas atmosphere.

(57) <Lithium Ion Secondary Battery>

(58) A lithium ion secondary battery according to one aspect of the present invention includes the positive electrode, a negative electrode, and a nonaqueous electrolyte, and includes components essential for a general lithium ion secondary battery.

(59) <Applications of Lithium Ion Secondary Battery>

(60) Applications of the lithium ion secondary battery are not particularly limited as long as the battery can be used as a drive power source or a power storage source for a machine, an apparatus, an instrument, a device, or a combined system thereof.

(61) As exemplary application examples of the lithium ion secondary battery, portable electronic devices such as a mobile phone, a smartphone, a laptop, and a personal digital assistant (PDA) which include the lithium ion secondary battery as a drive power source.

(62) FIG. 1 shows a block diagram of main functions when a mobile phone is used as an exemplary example of an electronic device.

(63) A mobile phone 10 includes a battery 1 including at least one lithium ion secondary battery of the present invention, a control unit 2, a display unit 3, an operation unit 4, a communication unit 5, and an antenna 6.

(64) The control unit 2 includes a CPU and a memory, and controls various devices to be mounted.

(65) The display unit 3 displays various types of information such as operation menus, the operation unit 4 is an input interface for performing operations of the mobile phone, and an input from the operation unit 4 is processed by the control unit 2 and an operation of the mobile phone is performed. The communication unit 5 performs wireless communication with a mobile phone base station through the antenna 6.

(66) FIG. 2 shows a schematic plan view of a drive system in which an electric vehicle is exemplified as a vehicle as another application of the lithium ion secondary battery.

(67) An electric vehicle 20 includes a battery module 11 including at least one lithium ion secondary battery of the present invention, an inverter 12, a motor 13, and a control unit 14.

(68) The electric vehicle 20 is driven when power is supplied from the battery module 11 to the motor 13 through the inverter 12. Power regenerated by the motor 13 during deceleration is stored in the battery module 11. The control unit 14 controls the inverter 12 so that torque is output in the same direction as rotation of a wheel 15 when an accelerator pedal is operated, and controls the inverter 12 so that torque is output in a direction opposite to a direction of rotation of a wheel when a brake pedal is operated.

(69) While FIG. 2 shows an exemplary case in which the battery is applied to the electric vehicle, the battery can be applied as a storage battery for storing power for running in a hybrid vehicle including a motor for running and an engine or a storage battery for storing power for accessory driving. The battery can also be applied as a storage battery for storing power for accessory driving in an engine vehicle. In this case, a storage battery for storing power for accessory driving is charged by power generated by an alternator connected to the engine.

EXAMPLES

(70) While the present invention will be described below in detail with reference to examples, the present invention is not limited to such examples.

Example 1-1

(71) Li.sub.0.6Ti.sub.0.2Mn.sub.0.2O corresponding to General Formula:
Li.sub.xTi.sub.2x-1Mn.sub.2-3xO (x=0.6)

(72) In order to obtain Li.sub.0.6Ti.sub.0.2Mn.sub.0.2O, Li.sub.2CO.sub.3 (commercially available from Wako Pure Chemical Corporation), TiO.sub.2 (commercially available from Kanto Chemical Co., Inc), and Mn.sub.2O.sub.3 (obtained by calcining manganese carbonate (commercially available from Kishida Chemical Co., Ltd.) at 700 C.) were weighed out at a molar ratio of 1.5:1:0.5. Then, the weighed out powders were mixed so that they became sufficiently uniform, and were then pelletized, and calcined at 900 C. for 12 hours, and thereby Li.sub.0.6Ti.sub.0.2Mn.sub.0.2O was obtained. In this case, a calcination atmosphere was an inert gas atmosphere.

(73) Next, the obtained powders were put into a pot made of zirconia into which a ball made of zirconia was added, set in a planetary ball mill (model number pluverisette 7 commercially available from FRITSCH), and mixed at 300 rpm for 12 hours. FIG. 3 is a microscopic image of a substance after a positive electrode active material for a lithium ion secondary battery is ground by ball milling when a positive electrode for the lithium ion secondary battery is produced.

(74) FIG. 4 shows X-ray diffraction images before and after ball milling was performed on the powder of the composite oxide obtained in Example 1-1. The horizontal axis represents a diffraction angle (2) and the vertical axis represents an intensity. It was confirmed that a crystal structure of the composite oxide obtained in Example 1 from the X-ray diffraction image was a rock salt type structure. In addition, the composition was analyzed by inductivity coupled plasma (ICP) analysis, and it was confirmed that the composition was Li.sub.0.6Ti.sub.0.2Mn.sub.0.2O (x=0.6).

(75) (Evaluation of Battery Characteristics)

(76) A bipolar electrochemical cell for evaluation was produced as follows using the obtained composite oxide Li.sub.0.6Ti.sub.0.2Mn.sub.0.2O (x=0.6) as a positive electrode active material for a lithium ion secondary battery, and battery characteristics thereof were evaluated.

(77) First, the obtained positive electrode active material Li.sub.0.6Ti.sub.0.2Mn.sub.0.2O (x=0.6) and acetylene black (AB) as a conductive material were mixed at a weight ratio of 80:20. A polyvinylidene fluoride (PVDF) binder that was dissolved in N-methyl pyrrolidone (NMP) was added to this mixture to prepare a slurry. In this slurry, a weight ratio of positive electrode active material:AB:PVDF was 76.5:13.5:10. This slurry was applied to an aluminum foil as a current collector and dried, and pressing was then performed to produce a positive electrode.

(78) A bipolar electrochemical cell for evaluation in which a counter electrode was a lithium foil was produced using this positive electrode.

(79) In this electrochemical cell, a solution in which 1M-LiPF.sub.6 was dissolved in EC/DMC (volume ratio of 1:1) was used as an electrolytic solution, and a charging and discharging test was performed. The charging and discharging test was performed at 50 C., a current density of 5 mA/g, and in a voltage range of 1.5 to 4.8 V.

(80) FIG. 5 shows charging and discharging characteristics of an electrochemical cell obtained using the composite oxide Li.sub.0.6Ti.sub.0.2Mn.sub.0.2O (x=0.6) of Example 1-1 as a positive electrode active material. Curves upward to the right correspond to charging curves and curves downward to the right correspond to discharging curves.

(81) Large charging and discharging capacities in which a charging capacity was 350 mAh/g and a discharging capacity was 315 mAh/g in the first cycle were obtained. The initial charging capacity of 350 mAh/g was a very large value corresponding to about 89% of the Li-based theoretical capacity of 394.9 mAh/g. These large charging and discharging capacities were caused by oxidation reduction reactions of oxide ions (O.sup.2/O.sub.2.sup.2).

(82) FIG. 6 shows evaluation results of a capacity retention characteristic of a discharging capacity of an electrochemical cell using the composite oxide Li.sub.0.6Ti.sub.0.2Mn.sub.0.2O (x=0.6) of Example 1-1 as a positive electrode active material. Charging and discharging capacities in cycles are shown when charging and discharging were repeated over 4 cycles at a current density of 5 mA/g and in a voltage range of 1.5 to 4.8 V. The discharging capacity in the fourth cycle was 300 mAh/g showing a discharging capacity of 95% of the discharging capacity in the first cycle, and a high discharging capacity retention rate was shown.

Example 1-2

(83) Example 1-2 was different from Example 1-1 only in that charging and discharging characteristics were measured at a current density increased to 10 mA/g and the other conditions were the same as those in Example 1-1. FIG. 7 shows charging and discharging characteristics of an electrochemical cell measured under conditions of Example 1-2 using a composite oxide Li.sub.0.6Ti.sub.0.2Mn.sub.0.2O (x=0.6) as a positive electrode active material. Curves upward to the right correspond to charging curves and curves downward to the right correspond to discharging curves.

(84) Under conditions of Example 1-2 also, similarly to Example 1-1, large charging and discharging capacities and a high discharging capacity retention rate were shown. A charging capacity was 350 mAh/g and a discharging capacity was 300 mAh/g in the first cycle. In addition, even after charging and discharging were repeated over 5 cycles, a high discharging capacity retention rate of 92% was shown. That is, even if the current density was high, an electrochemical cell using the composite oxide Li.sub.0.6Ti.sub.0.2Mn.sub.0.2O (x=0.6) as a positive electrode active material functioned normally.

Example 1-3

(85) Example 1-3 was different from Example 1-1 only in that charging and discharging characteristics were measured at a measurement temperature that was room temperature (25 C.) and the other conditions were the same as those in Example 1-1. FIG. 8 shows charging and discharging characteristics of an electrochemical cell measured under conditions of Example 1-3 using a composite oxide Li.sub.0.6Ti.sub.0.2Mn.sub.0.2O (x=0.6) as a positive electrode active material. Curves upward to the right correspond to charging curves and curves downward to the right correspond to discharging curves.

(86) Under conditions of Example 1-3, a charging capacity was 275 mAh/g and a discharging capacity was 215 mAh/g in the first cycle. While charging and discharging characteristics were lowered when the measurement temperature decreased, sufficiently high charging and discharging characteristics were shown. In addition, even after charging and discharging were repeated over 5 cycles, the discharging capacity did not largely decrease and a high discharging capacity retention rate of 93% was shown.

(87) FIG. 9 shows evaluation results of capacity retention characteristics of a discharging capacity of an electrochemical cell under conditions of Example 1-3 using a composite oxide Li.sub.0.6Ti.sub.0.2Mn.sub.0.2O (x=0.6) as a positive electrode active material.

Example 2

(88) Li.sub.0.55Ti.sub.0.1Mn.sub.0.35O corresponding to General Formula:
Li.sub.xTi.sub.2x-1Mn.sub.2-3xO (x=0.55)

(89) Li.sub.0.55Ti.sub.0.1Mn.sub.0.35O was prepared in the same manner as in a composite oxide Li.sub.0.6Ti.sub.0.2Mn.sub.0.2O (x=0.6) prepared in Example 1-1. Li.sub.2CO.sub.3, TiO.sub.2, and Mn.sub.2O.sub.3 were weighed out at a molar ratio of 1.1:0.4:0.7. Then, the weighed out powders were mixed so that they became sufficiently uniform, and were then pelletized, and calcined at 900 C. for 12 hours, and thereby Li.sub.0.55Ti.sub.0.1Mn.sub.0.35O was obtained. In this case, the calcination atmosphere was an inert gas atmosphere.

(90) The weighed out sample was calcined at 900 C. for 12 hours, and the calcined sample was finely ground using a ball mill under the same conditions as in Example 1-1.

(91) FIG. 10 shows X-ray diffraction images before and after ball milling was performed on the powder of the composite oxide obtained in Example 2. The horizontal axis represents a diffraction angle (2) and the vertical axis represents an intensity. It was confirmed that a crystal structure of the composite oxide obtained in Example 2 from the X-ray diffraction image was a rock salt type structure. In addition, the composition was analyzed by inductivity coupled plasma (ICP) analysis and it was confirmed that the composition was Li.sub.0.55Ti.sub.0.1Mn.sub.0.35O (x=0.55).

(92) FIG. 11 shows charging and discharging characteristics of an electrochemical cell obtained using a composite oxide Li.sub.0.55Ti.sub.0.1Mn.sub.0.35O (x=0.55) of Example 2 as a positive electrode active material. A curve upward to the right corresponds to a charging curve and a curve downward to the right corresponds to a discharging curve. Charging and discharging capacities measured under conditions of a current density of 10 mA/g, a voltage range of 1.5 to 4.8 V, and a measurement temperature of 50 C. are shown.

(93) As shown in FIG. 11, large charging and discharging capacities in which a charging capacity was 260 mAh/g and a discharging capacity was 230 mAh/g in the first cycle were obtained. An initial charging capacity of 260 mAh/g corresponded to about 71% of a Li-based theoretical capacity of 394.9 mAh/g, which indicated a high value. The large charging and discharging capacities were caused by oxidation reduction reactions of oxide ions (O.sup.2/O.sub.2.sup.2).

Example 3

(94) Li.sub.0.62Ti.sub.0.245Mn.sub.0.135O corresponding to General Formula:
Li.sub.xTi.sub.2x-1Mn.sub.2-3xO (x=0.62)

(95) Li.sub.0.62Ti.sub.0.245Mn.sub.0.135O was prepared in the same manner as in Example 1-1 in which a composite oxide Li.sub.0.6Ti.sub.0.2Mn.sub.0.2O (x=0.6) was prepared. Li.sub.2CO.sub.3, TiO.sub.2, and Mn.sub.2O.sub.3 were weighed out at a molar ratio of 1.24:0.96:0.27. Then, the weighed out powders were mixed so that they became sufficiently uniform, and were then pelletized, and calcined at 900 C. for 12 hours, and thereby Li.sub.0.62Ti.sub.0.245Mn.sub.0.135O was obtained. In this case, a calcination atmosphere was an inert gas atmosphere.

(96) The weighed out sample was calcined at 900 C. for 12 hours, and the calcined sample was finely ground using a ball mill under the same conditions as in Example 1-1.

(97) FIG. 12 shows X-ray diffraction images before and after ball milling was performed on the powder of the composite oxide obtained in Example 3. The horizontal axis represents a diffraction angle (2) and the vertical axis represents an intensity. It was confirmed that a crystal structure of the composite oxide obtained in Example 2 from the X-ray diffraction image was a rock salt type structure. In addition, the composition was analyzed by inductivity coupled plasma (ICP) analysis and it was confirmed that the composition was Li.sub.0.62Ti.sub.0.245Mn.sub.0.135O (x=0.62).

(98) FIG. 13 shows charging and discharging characteristics of an electrochemical cell obtained using a composite oxide Li.sub.0.62Ti.sub.0.245Mn.sub.0.135O (x=0.62) of Example 3 as a positive electrode active material. A curve upward to the right corresponds to a charging curve and a curve downward to the right corresponds to a discharging curve. Charging and discharging capacities measured under conditions of a current density of 10 mA/g, a voltage range of 1.5 to 4.8 V, and a measurement temperature of 50 C. are shown.

(99) As shown in FIG. 13, large charging and discharging capacities in which a charging capacity was 350 mAh/g and a discharging capacity was 280 mAh/g in the first cycle were obtained. An initial charging capacity of 350 mAh/g corresponded to about 89% of a Li-based theoretical capacity of 394.9 mAh/g, which indicated a very high value. The large charging and discharging capacities were caused by oxidation reduction reactions of oxide ions (O.sup.2/O.sub.2.sup.2).

(100) Based on results of Example 1-1, Example 2, and Example 3, even if a composite oxide in which a range of x in General Formula: Li.sub.xTi.sub.2x-1Mn.sub.2-3xO was changed was used as a positive electrode material, a rock salt type structure was maintain and high charging and discharging characteristics were exhibited. In addition, comparing Example 2 and Example 3, when a compositional proportion of Ti was higher, the contribution of oxide ions to oxidation reduction in charge compensation according to movement of lithium ions during charging and discharging was greater and it was possible to obtain high charging and discharging characteristics.

Reference Example 1

(101) Li.sub.0.625Ti.sub.0.1Nb.sub.0.075Mn.sub.0.2O corresponding to General Formula:
Li.sub.xTi.sub.yMn.sub.(3-y-4x)/2Nb.sub.(2x-y-1)/2O (x=0.625,y=0.1)

(102) Li.sub.0.625Ti.sub.0.1Nb.sub.0.075Mn.sub.0.2O was prepared in the same manner as in Example 1-1 in which a composite oxide Li.sub.0.6Ti.sub.0.2Mn.sub.0.2O (x=0.6) was prepared and by additionally adding Nb.sub.2O.sub.5 (commercially available from Wako Pure Chemical Corporation). Li.sub.2CO.sub.3, TiO.sub.2, Mn.sub.2O.sub.3, and Nb.sub.2O.sub.5 were weighed out at a molar ratio of 1.25:0.4:0.4:0.15. Then, the weighed out powders were mixed so that they became sufficiently uniform, and were then pelletized, and calcined at 900 C. for 12 hours, and thereby Li.sub.0.625Ti.sub.0.1Nb.sub.0.075Mn.sub.0.2O was obtained. In this case, a calcination atmosphere was an inert gas atmosphere.

(103) FIG. 14 shows X-ray diffraction images before and after ball milling is performed on a powder of a composite oxide obtained in Reference Example 1. The horizontal axis represents a diffraction angle (2) and the vertical axis represents an intensity. It was confirmed that a crystal structure of the composite oxide obtained in Reference Example 1 from the X-ray diffraction image was a rock salt type structure. In addition, the composition was analyzed by inductivity coupled plasma (ICP) analysis, and it was confirmed that the composition was Li.sub.0.625Ti.sub.0.1Nb.sub.0.075Mn.sub.0.2O (x=0.625, y=0.1).

(104) FIG. 15 shows charging and discharging characteristics of an electrochemical cell obtained using a composite oxide Li.sub.0.625 Ti.sub.0.1Nb.sub.0.075Mn.sub.0.2O (x=0.625, y=0.1) of Reference Example 1 as a positive electrode active material. A curve upward to the right corresponds to a charging curve and a curve downward to the right corresponds to a discharging curve. Charging and discharging capacities measured under conditions of a current density of 10 mA/g, a voltage range of 1.5 to 4.8 V, and a measurement temperature of 50 C. are shown.

(105) As shown in FIG. 15, large charging and discharging capacities in which a charging capacity was 340 mAh/g and a discharging capacity was 310 mAh/g in the first cycle were obtained. The large charging and discharging capacities were caused by oxidation reduction reactions of oxide ions (O.sup.2/O.sub.2.sup.2).

(106) As shown in Reference Example 1, the composition of General Formula (2) in which a part of the composition of General Formula (1) shown in Example 1-1 to Example 3 was substituted with Nb also exhibited high charging and discharging characteristics.

EXPLANATION OF REFERENCES

(107) 1 Battery 2 Control unit 3 Display unit 4 Operation unit 5 Communication unit 6 Antenna 10 Mobile phone 11 Battery module 12 Inverter 13 Monitor 14 Control unit 15 Wheel 20 Electric vehicle