JP6252603B2 - Electrical device - Google Patents

Description

  The present invention relates to electrical devices. The electric device according to the present invention is used, for example, as a secondary battery, a capacitor or the like as a driving power source or auxiliary power source for motors of vehicles such as electric vehicles, fuel cell vehicles, and hybrid electric vehicles.

  In recent years, in order to cope with global warming, reduction of the amount of carbon dioxide is eagerly desired. In the automobile industry, there is a great expectation for reducing carbon dioxide emissions by introducing electric vehicles (EV) and hybrid electric vehicles (HEV). Electric devices such as secondary batteries for motor drive that hold the key to their practical application. Is being actively developed.

  As a secondary battery for driving a motor, it is required to have extremely high output characteristics and high energy as compared with a consumer lithium ion secondary battery used in a mobile phone, a notebook personal computer or the like. Therefore, lithium ion secondary batteries having the highest theoretical energy among all the batteries are attracting attention, and are currently being developed rapidly.

  Generally, a lithium ion secondary battery includes a positive electrode in which a positive electrode active material or the like is applied to both surfaces of a positive electrode current collector using a binder, and a negative electrode in which a negative electrode active material or the like is applied to both surfaces of a negative electrode current collector using a binder. However, it has the structure connected through an electrolyte layer and accommodated in a battery case.

Conventionally, carbon / graphite-based materials that are advantageous in terms of charge / discharge cycle life and cost have been used for negative electrodes of lithium ion secondary batteries. However, since carbon / graphite-based negative electrode materials are charged / discharged by occlusion / release of lithium ions into / from graphite crystals, the charge / discharge capacity of the theoretical capacity 372 mAh / g or more obtained from LiC ₆ which is the maximum lithium-introduced compound. There is a disadvantage that cannot be obtained. For this reason, it is difficult to obtain a capacity and energy density that satisfy the practical use level of the vehicle application with the carbon / graphite negative electrode material.

In contrast, a battery using a SiO _x (0 <x <2) material that forms a compound with Li in the negative electrode has an improved energy density as compared with a conventional carbon / graphite negative electrode material. Expected as a material. For example, in a silicon oxide having a chemical composition represented by SiO _x , when viewed microscopically, Si (single crystal nanoparticles) and amorphous SiO ₂ exist in phase separation.

Silicon oxide has a tetrahedral structure as a unit structure, and silicon oxides (intermediate oxides) other than SiO ₂ correspond to the number of oxygen at the apex of the tetrahedron, 1, 2 and 3, respectively. _Although they can be expressed as ₂ O, SiO and Si ₂ O ₃ , these intermediate oxides are thermodynamically unstable and are extremely difficult to exist as single crystals. Therefore, SiO _x is composed of an amorphous structure in which unit structures are irregularly arranged, and this amorphous structure is an amorphous structure in which a plurality of amorphous compounds are formed without forming an interface. The structure is mainly composed of a homogeneous amorphous structure portion. Therefore, SiO _x has a structure in which Si nanoparticles are dispersed in amorphous SiO ₂ .

In the case of SiO _x , only Si can participate in charging / discharging, and SiO ₂ does not participate in charging / discharging. Therefore, SiO _x represents the average composition thereof. In SiO _x , Si absorbs and releases _4.4 mol of lithium ions per mol as in reaction formula (A), and a reversible capacity component of Li ₂₂ Si ₅ (= Li _4.4 Si) with a theoretical capacity of 4200 mAh / g is obtained. On the other hand, Li ₄ SiO ₄ causes SiO to absorb and release 4.3 mol of lithium ions per mol as shown in the reaction formula (B), and causes irreversible capacity together with Li _4.4 Si during the first Li storage. The point of generating is a big problem.

By the way, as a lithium silicate compound containing Li, for example, Li _y SiO _x such as Li ₄ SiO ₄ , Li ₂ SiO ₃ , Li ₂ Si ₂ O ₅ , Li ₂ Si ₃ O ₈ , Li ₆ Si ₄ O _11, etc. (0 <y, 0 <x <2), but Li _y SiO _x has extremely low electron conductivity, and furthermore, since SiO ₂ does not have electron conductivity, the resistance of the negative electrode increases. There is. As a result, it is extremely difficult to desorb and insert lithium ions into the negative electrode active material.

  However, a lithium ion secondary battery using a material that is alloyed with Li for the negative electrode has a large expansion and contraction in the negative electrode during charge and discharge. For example, the volume expansion when lithium ions are occluded is about 1.2 times in graphite materials, whereas in Si materials, when Si and Li are alloyed, the amorphous state transitions to the crystalline state, resulting in a large volume change. (Approximately 4 times), there was a problem of reducing the cycle life of the electrode. In the case of the Si negative electrode active material, the battery capacity and the cycle durability are in a trade-off relationship, and there is a problem that it is difficult to improve the high cycle durability while exhibiting a high capacity.

In order to solve such a problem, a negative electrode for a lithium ion secondary battery containing SiO _x and a graphite material has been proposed (see, for example, Patent Document 1). In the invention described in Patent Document 1, paragraph “0018” describes that, by minimizing the content of SiO _x , good cycle life is exhibited in addition to high capacity.

Special table 2009-517850

In the case of a lithium ion secondary battery using a negative electrode containing SiO _x and a carbon material described in Patent Document 1, it is said that good cycle characteristics can be exhibited. However, according to the study by the present inventors, when such a negative electrode is combined with a positive electrode using a solid solution positive electrode active material, the high capacity characteristics characteristic of the solid solution positive electrode active material cannot be fully utilized. As for the rate characteristics, it was found difficult to achieve sufficient performance.

  Therefore, the present invention is satisfactory in rate characteristics while fully utilizing the high capacity characteristics that are characteristic of solid solution positive electrode active materials in electrical devices such as lithium ion secondary batteries having positive electrodes using solid solution positive electrode active materials. The object is to provide a means to achieve the desired performance.

In order to solve the above-mentioned problems, the present inventors have conducted intensive research. As a result, a negative electrode containing a negative electrode active material obtained by mixing SiO _x and a carbon material, and a positive electrode containing a Mn-containing solid solution positive electrode active material in which Mn is substituted with a predetermined element are used. The inventors have found that the above problem can be solved by controlling the coating amount (weight per unit area) of the material layer to a predetermined value, and have completed the present invention.

  That is, the present invention includes a positive electrode in which a positive electrode active material layer including a positive electrode active material is formed on the surface of a positive electrode current collector, and a negative electrode active material layer including a negative electrode active material on the surface of the negative electrode current collector. The present invention relates to an electric device having a power generation element including a negative electrode and a separator.

And the application quantity of the said negative electrode active material layer is 3-11 mg / cm < ² >. Moreover, the said negative electrode active material layer contains the negative electrode active material represented by following formula (1).

In the formula, SiO _x is a mixture of amorphous SiO ₂ particles and Si particles, x represents the number of oxygen satisfying the valence of Si, α (SiO _x ) and β (carbon material) are negative electrode active material layers Represents the wt% of the SiO _x and carbon material in which, respectively , 80 ≦ α (SiO _x ) + β (carbon material) ≦ 98, 3 ≦ α (SiO _x ) ≦ 40, 40 ≦ β (carbon material) ≦ 95.

  Furthermore, the positive electrode active material layer contains a positive electrode active material represented by the following formula (2).

In the formula, f (solid solution positive electrode active material) represents the weight% of the solid solution positive electrode active material in the positive electrode active material layer, and 80 ≦ f (solid solution positive electrode active material) ≦ 98.

  At this time, the solid solution positive electrode active material has a composition represented by the following formula (3).

  In the formula, X is at least one selected from the group consisting of Ti, Zr and Nb, and 0.01 ≦ e ≦ 0.4, a + b + c + d + e = 1.5, 0.1 ≦ d ≦ 0.4, 1.1 ≦ [a + b + c + e] ≦ 1.4, and z represents the number of oxygen satisfying the valence.

  According to the present invention, by using the positive electrode active material as a solid solution material having a predetermined composition, it is possible to significantly reduce the decrease in the initial discharge capacity due to the initial irreversible capacity of the negative electrode active material. As a result, the electrical device according to the present invention can achieve satisfactory performance in terms of rate characteristics while fully utilizing the high capacity characteristics that are characteristic of the solid solution positive electrode active material.

1 is a schematic cross-sectional view showing the basic configuration of a non-aqueous electrolyte lithium ion secondary battery that is not a flat type (stacked type) bipolar type, which is an embodiment of the electrical device according to the present invention. It is a perspective view showing the appearance of a flat lithium ion secondary battery which is a typical embodiment of an electric device according to the present invention. It is a chart which shows the X-ray-diffraction pattern of the solid solution positive electrode active material C0 which does not contain Ti. 2 is a chart showing an X-ray diffraction pattern of the solid solution positive electrode active material C1 obtained in Example 1. FIG.

According to one embodiment of the present invention, a positive electrode in which a positive electrode active material layer containing a positive electrode active material is formed on the surface of a positive electrode current collector, and a negative electrode active material layer containing a negative electrode active material on the surface of the negative electrode current collector are provided. An electric device having a power generation element including a formed negative electrode and a separator,
The coating amount of the negative electrode active material layer is 3 to 11 mg / cm ² ,
The negative electrode active material layer has the following formula (1):

In the formula, SiO _x is a mixture of amorphous SiO ₂ particles and Si particles, x represents the number of oxygen satisfying the valence of Si, α (SiO _x ) and β (carbon material) are negative electrode active material layers Represents the weight percentage of SiO _x and carbon material in each of the following : 80 ≦ α (SiO _x ) + β (carbon material) ≦ 98, 3 ≦ α (SiO _x ) ≦ 40, 40 ≦ β (carbon material) ≦ 95,
Containing a negative electrode active material represented by
The positive electrode active material layer has the following formula (2):

In the formula, f (solid solution positive electrode active material) represents the weight% of the solid solution positive electrode active material in the positive electrode active material layer, and 80 ≦ f (solid solution positive electrode active material) ≦ 98.
In this case, the solid solution positive electrode active material is represented by the following formula (3):

In the formula, X is at least one selected from the group consisting of Ti, Zr and Nb, and 0.01 ≦ e ≦ 0.4, a + b + c + d + e = 1.5, 0.1 ≦ d ≦ 0.4, 1.1 ≦ [a + b + c + e] ≦ 1.4, and z represents the number of oxygen satisfying the valence.
An electrical device having the composition represented by:

  Hereinafter, the basic configuration of the electric device according to the present invention will be described. In the present embodiment, a lithium ion secondary battery will be described as an example of an electric device.

  First, in the lithium ion secondary battery using the electrical device according to the present invention, the voltage of the cell (single cell layer) is large, and high energy density and high output density can be achieved. Therefore, the lithium ion secondary battery of the present embodiment is excellent as a vehicle driving power source or an auxiliary power source. As a result, it can be suitably used as a lithium ion secondary battery for a vehicle driving power source or the like. In addition to this, the present invention can be sufficiently applied to lithium ion secondary batteries for portable devices such as mobile phones.

  When the lithium ion secondary battery is distinguished by its form / structure, it can be applied to any conventionally known form / structure such as a stacked (flat) battery or a wound (cylindrical) battery. Is. By adopting a stacked (flat) battery structure, long-term reliability can be secured by a sealing technique such as simple thermocompression bonding, which is advantageous in terms of cost and workability.

  Moreover, when viewed in terms of electrical connection form (electrode structure) in a lithium ion secondary battery, it can be applied to both non-bipolar (internal parallel connection type) batteries and bipolar (internal series connection type) batteries. Is.

  When distinguished by the type of electrolyte layer in the lithium ion secondary battery, a solution electrolyte type battery using a solution electrolyte such as a nonaqueous electrolyte solution for the electrolyte layer, a polymer battery using a polymer electrolyte for the electrolyte layer, etc. It can be applied to any conventionally known electrolyte layer type. The polymer battery is further divided into a gel electrolyte type battery using a polymer gel electrolyte (also simply referred to as gel electrolyte) and a solid polymer (all solid) type battery using a polymer solid electrolyte (also simply referred to as polymer electrolyte). It is done.

  Therefore, in the following description, a non-bipolar (internal parallel connection type) lithium ion secondary battery will be described with reference to the drawings as an example of the lithium ion secondary battery of the present embodiment. However, the technical scope of the electric device according to the present invention and the lithium ion secondary battery according to the present embodiment should not be limited to these.

<Overall battery structure>
FIG. 1 schematically shows the overall structure of a flat (stacked) lithium ion secondary battery (hereinafter also simply referred to as “stacked battery”), which is a typical embodiment of the electrical device of the present invention. FIG.

  As shown in FIG. 1, the stacked battery 10 of the present embodiment has a structure in which a substantially rectangular power generation element 21 in which a charge / discharge reaction actually proceeds is sealed inside a laminate sheet 29 that is an exterior body. . Here, in the power generation element 21, the positive electrode in which the positive electrode active material layer 13 is disposed on both surfaces of the positive electrode current collector 11, the electrolyte layer 17, and the negative electrode active material layer 15 is disposed on both surfaces of the negative electrode current collector 12. It has a configuration in which a negative electrode is laminated. Specifically, the negative electrode, the electrolyte layer, and the positive electrode are laminated in this order so that one positive electrode active material layer 13 and the negative electrode active material layer 15 adjacent thereto face each other with the electrolyte layer 17 therebetween. .

  Thereby, the adjacent positive electrode, electrolyte layer, and negative electrode constitute one unit cell layer 19. Therefore, it can be said that the stacked battery 10 shown in FIG. 1 has a configuration in which a plurality of single battery layers 19 are stacked and electrically connected in parallel. The positive electrode current collector 13 on the outermost layer located on both outermost layers of the power generating element 21 is provided with the positive electrode active material layer 13 only on one side, but the active material layer may be provided on both sides. . That is, instead of using a current collector dedicated to the outermost layer provided with an active material layer only on one side, a current collector having an active material layer on both sides may be used as it is as an outermost current collector. Further, by reversing the arrangement of the positive electrode and the negative electrode as compared with FIG. 1, the outermost negative electrode current collector is positioned on both outermost layers of the power generation element 21, and one side of the outermost negative electrode current collector or A negative electrode active material layer may be disposed on both sides.

  The positive electrode current collector 11 and the negative electrode current collector 12 are attached to a positive electrode current collector plate 25 and a negative electrode current collector plate 27 that are electrically connected to the respective electrodes (positive electrode and negative electrode), and are sandwiched between end portions of the laminate sheet 29. Thus, it has a structure led out of the laminate sheet 29. The positive electrode current collector plate 25 and the negative electrode current collector plate 27 are ultrasonically welded to the positive electrode current collector 11 and the negative electrode current collector 12 of each electrode via a positive electrode lead and a negative electrode lead (not shown), respectively, as necessary. Or resistance welding or the like.

  The lithium ion secondary battery according to the present embodiment is characterized by the configuration of the positive electrode and the negative electrode. Hereinafter, main components of the battery including the positive electrode and the negative electrode will be described.

<Active material layer>
The active material layers (13, 15) contain an active material, and further contain other additives as necessary.

[Positive electrode active material layer]
The positive electrode active material layer 13 includes at least a positive electrode active material (also referred to as “solid solution positive electrode active material” in the present specification) made of a solid solution material.

(Solid solution positive electrode active material)
The solid solution positive electrode active material has a composition represented by the following formula (3).

  In the formula (3), X is at least one selected from the group consisting of Ti, Zr and Nb, and 0.01 ≦ e ≦ 0.4, a + b + c + d + e = 1.5, 0.1 ≦ d ≦ 0 .4, 1.1 ≦ [a + b + c + e] ≦ 1.4, and z represents the number of oxygens satisfying the valence.

  Furthermore, this solid solution positive electrode active material was measured at 20-23 °, 35-40 ° (101), 42-45 ° (104) and 64-65 (108) / 65-66 (X-ray diffraction (XRD) measurement). 110) preferably has a diffraction peak indicating a rock salt type layered structure. At this time, in order to surely obtain the effect of improving the cycle characteristics, those having substantially no peak attributed to other than the diffraction peak of the rock salt type layered structure are preferable. More preferably, one having three diffraction peaks at 35-40 ° (101) and one diffraction peak at 42-45 ° (104) is suitable. However, as long as it belongs to a diffraction peak of a rock salt type layered structure, it does not necessarily have to be counted as three and one peak, respectively. The X-ray diffraction measurement shall employ the measurement method described in the examples described later. In addition, the notation of 64-65 (108) / 65-66 (110) has two peaks close to 64-65 and 65-66. It is meant to include.

The solid solution positive electrode active material having the composition represented by the composition formula (3) preferably has a plurality of specific diffraction peaks in the X-ray diffraction (XRD) measurement. The solid solution positive electrode active material of the above composition formula is a solid solution system of Li ₂ MnO ₃ and LiMnO ₂ , and the diffraction peak at 20-23 ° is characteristic of Li ₂ MnO ₃ among the plurality of diffraction peaks specified above. Superlattice diffraction peak. Also, the diffraction peaks of 36.5-37.5 ° (101), 44-45 ° (104), and 64-65 (108) / 65-66 (110) are generally in the rock salt type layered structure of LiMnO _2. It is characteristic. Moreover, in this embodiment, it is preferable to have three diffraction peaks at 35-40 ° (101) and one diffraction peak at 42-45 ° (104) as a part of diffraction peaks showing a rock salt type layered structure. It is preferable that the solid solution positive electrode active material of the present embodiment does not include those having a peak other than a diffraction peak showing a rock salt type layered structure, for example, other peaks derived from impurities or the like, in these angular ranges. When such other peaks exist, it means that a structure other than the rock salt type layered structure is included in the positive electrode active material. If the structure other than the rock salt type layered structure is not included, the effect of improving the cycle characteristics can be surely obtained.

In the solid solution positive electrode active material according to the present embodiment, at least one of Ti, Zr, and Nb is dissolved in a transition metal layer made of Ni, Co, and Mn by substituting Mn ⁴⁺ to form a rock salt type It is considered that a layered structure is formed. Since at least one kind of Ti, Zr and Nb is dissolved, the crystal structure is stabilized, so that it is considered that elution of transition metals including Mn is suppressed during charging and discharging. As a result, even if charging / discharging is repeated, the capacity reduction of the battery can be prevented, and excellent cycle characteristics can be achieved. In addition, battery performance itself and durability can be improved. When the rock salt type layered structure is changed by elution of Mn, a spinel phase is usually formed, and the diffraction peak in the X-ray diffraction (XRD) measurement of the positive electrode active material represents the spinel phase. In the spinel phase, diffraction peaks appear at 35-36 ° (101) and 42.5-43.5 ° (104). In the solid solution positive electrode active material according to the present embodiment, it is considered that a spinel phase is not formed even after repeated charge and discharge, and a rock salt type layered structure is maintained. However, the present embodiment is not limited to the above consideration.

  Furthermore, it is preferable that the diffraction peak which shows the rock salt type | mold layered structure in this embodiment has shifted to the low angle side. That is, the solid solution positive electrode active material according to the present embodiment is 20-23 °, 35.5-36.5 ° (101), 43.5-44.5 ° (104) in X-ray diffraction (XRD) measurement. And preferably have diffraction peaks at 64-65 (108) / 65-66 (110). The shift of the diffraction peak to the lower angle side indicates that Ti and the like are more solid-dissolved in the positive electrode active material and substitutes Mn, which is considered to have a greater effect of suppressing Mn elution.

Furthermore, when Ti or the like substitutes Mn ⁴⁺ in the transition metal layer of the positive electrode active material and solid-dissolves, the covalent bond between the substitution element and oxygen becomes stronger, and the oxygen in the crystal lattice accompanying the oxidation of the transition metal becomes stronger. Separation can also be reduced. As a result, generation of oxygen gas can be suppressed and oxygen defects in the crystal structure can be reduced.

  Here, in the composition formula (3), a + b + c + e satisfies 1.1 ≦ [a + b + c + e] ≦ 1.4. Generally, nickel (Ni), cobalt (Co), and manganese (Mn) are known to contribute to capacity characteristics and output characteristics from the viewpoint of improving the purity of the material and improving the electronic conductivity. Ti or the like partially substitutes Mn in the crystal lattice. When 1.1 ≦ [a + b + c + e] ≦ 1.2, each element can be optimized and the capacity and output characteristics can be further improved. Therefore, when a positive electrode active material that satisfies this relationship is used in an electrical device such as a lithium ion secondary battery, it exhibits excellent initial charge / discharge efficiency while maintaining a high capacity by maintaining a high reversible capacity. It becomes possible.

  In the composition formula (3), the values of a, b and c are not particularly limited as long as the relationship of a + b + c + d + e = 1.5 and 1.1 ≦ [a + b + c + e] ≦ 1.4 is satisfied. However, a is preferably 0 <a <1.5, and more preferably 0.1 ≦ a ≦ 0.75. When a is in the above range, a secondary battery having a better capacity retention rate can be obtained. When a is not a ≦ 0.75, the crystal structure is not stabilized because nickel is contained in the positive electrode active material within the above range d on condition that nickel (Ni) is divalent. There is. On the other hand, when a ≦ 0.75, the crystal structure of the positive electrode active material tends to be a rock salt type layered structure.

  Furthermore, in the composition formula (3), b is preferably 0 <b <1.5, and more preferably 0.2 ≦ b ≦ 0.9. When b is in the above range, an electric device having a better capacity retention rate can be obtained. However, when b does not satisfy b ≦ 0.9, manganese is contained in the positive electrode active material within the above range d, provided that manganese is tetravalent, and nickel (Ni ), The crystal structure may not be stabilized. On the other hand, when b ≦ 0.9, the crystal structure of the positive electrode active material tends to be a rock salt type layered structure.

  In the composition formula (3), c is preferably 0 ≦ c <1.5. However, when c is not c ≦ 0.6, nickel and manganese are contained in the positive electrode active material within the above range d on condition that cobalt is trivalent. Further, cobalt (Co) is contained in the positive electrode active material within the above range d on condition that nickel (Ni) is divalent and manganese (Mn) is tetravalent. Therefore, the crystal structure of the positive electrode active material may not be stabilized. On the other hand, when c ≦ 0.6, the crystal structure of the positive electrode active material tends to be a rock salt type layered structure.

  In the composition formula (3), a + b + c + d + e = 1.5. By satisfying this formula, the crystal structure of the positive electrode active material can be stabilized.

In the composition formula (3), 0.1 ≦ d ≦ 0.4. When d is not 0.1 ≦ d ≦ 0.4, the crystal structure of the positive electrode active material may not be stabilized. On the contrary, when d is 0.1 ≦ d ≦ 0.4, the positive electrode active material tends to have a rock salt type layered structure. The range of d is more preferably 0.15 ≦ d ≦ 0.35. When d is 0.1 or more, the composition is less likely to be close to Li ₂ MnO ₃ and charge / discharge is facilitated, which is preferable.

In the composition formula (3), 0.01 ≦ e ≦ 0.4. When e is not 0.01 ≦ e ≦ 0.4, the element cannot be uniformly dissolved in the crystal structure, and the crystal structure cannot be stabilized. On the other hand, if e is 0.01 ≦ e ≦ 0.4, at least one of Ti, Zr, and Nb can sufficiently substitute Mn ^{4+ so} that elution is suppressed. More preferably, e satisfies 0.02 ≦ e ≦ 0.3, more preferably 0.025 ≦ e ≦ 0.25, and particularly preferably 0.03 ≦ e ≦ 0.2.

The ionic radius of each element is Mn ⁴⁺ 0.54０．５, Mn ⁴⁺ 0.54Å, Ti ⁴⁺ 0.61Å, Zr ⁴⁺ 0.72Å, Nb ⁵⁺ 0.64Å, and Ti, Zr and Nb are larger than Mn. ing. Therefore, as Mn ⁴⁺ in the positive electrode active material is replaced with Ti or the like, the crystal lattice expands, and the diffraction peak indicating the rock salt type layered structure shifts to a lower angle side. On the contrary, if the diffraction peak is shifted to a lower angle side, the substitution amount of Mn ⁴⁺ such as Ti is larger, and the crystal structure is easily stabilized. That is, elution of Mn at the time of charging / discharging is further suppressed, and the capacity reduction of the electric device can be more effectively prevented.

The specific surface area of the cathode active material is preferably 0.2~0.6m ² / g, more preferably 0.25~0.5m ² / g. A specific surface area of 0.2 m ² / g or more is preferable because sufficient battery output can be obtained. On the other hand, it is preferable that the specific surface area is 0.6 m ² / g or less because elution of manganese can be further suppressed. In addition, in this specification, the value measured by the method of an Example shall be employ | adopted as the value of a specific surface area unless there is particular notice.

  As an average particle diameter of a positive electrode active material, it is preferable that it is 10-20 micrometers, and it is more preferable that it is 12-18 micrometers. It is preferable that the average particle size is 10 μm or more because elution of manganese can be suppressed. On the other hand, when the average particle size is 20 μm or less, it is preferable that foil breakage, clogging, and the like can be suppressed in the application step to the current collector during the production of the positive electrode. The average particle diameter is measured by a laser diffraction / scattering particle size distribution measuring device. The average particle diameter can be measured, for example, using a particle size distribution analyzer (model LA-920) manufactured by Horiba.

  The solid solution positive electrode active material as described above can be prepared, for example, by the following method. That is, a first step of mixing at least one citrate of Ti, Zr, and Nb with an organic acid salt of a transition metal having a melting point of 100 ° C. to 350 ° C., and the mixture obtained in the first step at 100 ° C. A second step of melting at ˜350 ° C., a third step of pyrolyzing the melt obtained in the second step at a temperature higher than the melting point, and a second step of firing the pyrolyzate obtained in the third step. 4 steps. Hereinafter, each step will be described.

First Step In the first step, at least one citrate of Ti, Zr and Nb and an organic acid salt of a transition metal having a melting point of 100 ° C. to 350 ° C. are mixed. At least one citrate of Ti, Zr and Nb is preferably mixed in the form of an aqueous citric acid complex solution. The aqueous solution of at least one kind of citrate complex of Ti, Zr and Nb is not limited to the following, but it can be preferably prepared as follows.

  That is, anhydrous citric acid is dissolved in an organic solvent such as acetone, and at least one alkoxide of Ti, Zr, and Nb is added to the solution. At this time, the molar ratio of at least one of Ti, Zr and Nb to citric acid is preferably (1 / at least one of Ti, Zr and Nb) / citric acid being 1/1 to 1/2. When alkoxide is added, precipitation occurs in the solution, and the precipitate is filtered with suction. Next, water is added to the obtained precipitate, and the mixture is stirred and heated to 50 to 60 ° C. to dissolve. The amount of water is appropriately added so that the concentration of the aqueous citric acid complex solution is finally 1 to 10% by mass in terms of at least one oxide of Ti, Zr and Nb. This aqueous solution is allowed to stand for one day, and the precipitate is filtered to obtain an aqueous solution of at least one citrate complex of Ti, Zr and Nb as a filtrate.

  As at least one alkoxide of Ti, Zr and Nb, titanium tetraisopropoxide, zirconium tetraisopropoxide, niobium isopropoxide, titanium ethoxide, titanium n-propoxide, titanium butoxide, zirconium ethoxide, zirconium n- Examples thereof include propoxide, zirconium butoxide, niobium ethoxide, and niobium butoxide.

  Next, an organic acid salt of a transition metal having a melting point of 100 ° C. to 350 ° C. is added to the obtained aqueous solution of at least one kind of citric acid complex of Ti, Zr and Nb to obtain a mixture. The organic acid salt of transition metal having a melting point of 100 ° C. to 350 ° C. preferably includes nickel acetate, manganese acetate, cobalt acetate, manganese citrate and the like.

  Preferably, an organic acid salt of an alkali metal is further mixed into the aqueous solution of at least one kind of citric acid complex of Ti, Zr and Nb. Preferred examples of the organic acid salt of alkali metal include lithium acetate and lithium citrate. It is preferable to mix an alkali metal organic acid salt at this stage because the production method is simple.

Second Step The mixture obtained in the first step is melted at 100 to 350 ° C., preferably 200 to 300 ° C.

Third Step The heated melt (slurry) obtained in the second step is pyrolyzed at a temperature equal to or higher than the melting point of the organic acid salt of the transition metal used in the first step to obtain a pyrolyzate that is a dry powder. When the melting points of the organic acid salts of a plurality of transition metals are different from each other, they are thermally decomposed at a temperature equal to or higher than the highest melting point. More specifically, the melt can be heated and sprayed at 200 to 600 ° C., more preferably 200 to 400 ° C., with a spray device.

Fourth Step The pyrolyzate obtained in the third step is calcined at 600 to 1200 ° C., more preferably 800 to 1100 ° C. for 5 to 20 hours, preferably 10 to 15 hours. Temporary baking may be performed before baking. In that case, temporary baking can be performed at 200 to 700 ° C., more preferably 300 to 600 ° C. for 1 to 10 hours, and more preferably 2 to 6 hours. Thus, the positive electrode active material of this embodiment is obtained.

  In some cases, a positive electrode active material other than the solid solution positive electrode active material described above may be used in combination. In this case, preferably, from the viewpoint of capacity and output characteristics, a lithium-transition metal composite oxide is used in combination as the positive electrode active material. Of course, other positive electrode active materials may be used. When the optimum particle size is different for expressing the unique effect of each active material, the optimum particle size may be blended and used for expressing each unique effect. It is not always necessary to make the particle diameter uniform.

  Although the average particle diameter of the positive electrode active material contained in the positive electrode active material layer 13 is not particularly limited, it is preferably 1 to 30 μm and more preferably 5 to 20 μm from the viewpoint of increasing the output. In the present specification, the “particle diameter” refers to the outline of the active material particles (observation surface) observed using an observation means such as a scanning electron microscope (SEM) or a transmission electron microscope (TEM). It means the maximum distance among any two points. In this specification, the value of “average particle diameter” is the value of particles observed in several to several tens of fields using an observation means such as a scanning electron microscope (SEM) or a transmission electron microscope (TEM). The value calculated as the average value of the particle diameter shall be adopted. The particle diameters and average particle diameters of other components can be defined in the same manner.

  As described above, the positive electrode active material layer contains a positive electrode active material (solid solution positive electrode active material) represented by the following formula (2).

In the formula (2), f (solid solution positive electrode active material) represents the weight% of the solid solution positive electrode active material in the positive electrode active material layer, and 80 ≦ f (solid solution positive electrode active material) ≦ 98.

  As is clear from the formula (2), the content of the solid solution positive electrode active material in the positive electrode active material layer is essential to be 80 to 98% by weight, preferably 84 to 98% by weight.

  Moreover, it is preferable that a positive electrode active material layer contains a binder and a conductive support agent other than the solid solution positive electrode active material mentioned above. Further, if necessary, it further contains other additives such as an electrolyte (polymer matrix, ion-conductive polymer, electrolyte solution, etc.) and a lithium salt for increasing the ion conductivity.

(Binder)
Although it does not specifically limit as a binder used for a positive electrode active material layer, For example, the following materials are mentioned. Polyethylene, polypropylene, polyethylene terephthalate (PET), polyether nitrile, polyacrylonitrile, polyimide, polyamide, cellulose, carboxymethyl cellulose (CMC) and its salts, ethylene-vinyl acetate copolymer, polyvinyl chloride, styrene-butadiene rubber (SBR) ), Isoprene rubber, butadiene rubber, ethylene / propylene rubber, ethylene / propylene / diene copolymer, styrene / butadiene / styrene block copolymer and hydrogenated product thereof, styrene / isoprene / styrene block copolymer and hydrogenated product thereof Thermoplastic polymers such as products, polyvinylidene fluoride (PVdF), polytetrafluoroethylene (PTFE), tetrafluoroethylene-hexafluoropropylene copolymer (F P), tetrafluoroethylene / perfluoroalkyl vinyl ether copolymer (PFA), ethylene / tetrafluoroethylene copolymer (ETFE), polychlorotrifluoroethylene (PCTFE), ethylene / chlorotrifluoroethylene copolymer (ECTFE) ), Fluororesin such as polyvinyl fluoride (PVF), vinylidene fluoride-hexafluoropropylene-based fluororubber (VDF-HFP-based fluororubber), vinylidene fluoride-hexafluoropropylene-tetrafluoroethylene-based fluororubber (VDF-HFP) -TFE fluorine rubber), vinylidene fluoride-pentafluoropropylene fluorine rubber (VDF-PFP fluorine rubber), vinylidene fluoride-pentafluoropropylene-tetrafluoroethylene Fluorine rubber (VDF-PFP-TFE fluorine rubber), vinylidene fluoride-perfluoromethyl vinyl ether-tetrafluoroethylene fluorine rubber (VDF-PFMVE-TFE fluorine rubber), vinylidene fluoride-chlorotrifluoroethylene fluorine Examples thereof include vinylidene fluoride fluorine rubber such as rubber (VDF-CTFE fluorine rubber), epoxy resin, and the like. These binders may be used independently and may use 2 or more types together.

  The binder content in the positive electrode active material layer is preferably 1 to 10% by weight, more preferably 1 to 8% by weight.

(Conductive aid)
The conductive assistant refers to an additive that is blended in order to improve the conductivity of the positive electrode active material layer or the negative electrode active material layer. Examples of the conductive assistant include carbon black such as ketjen black and acetylene black. When the active material layer contains a conductive additive, an electronic network inside the active material layer is effectively formed, which can contribute to improvement of the output characteristics of the battery.

  The content of the conductive additive in the positive electrode active material layer is preferably 1 to 10% by weight, more preferably 1 to 8% by weight. By defining the blending ratio (content) of the conductive assistant within the above range, the following effects are exhibited. That is, the electron conductivity can be sufficiently ensured without hindering the electrode reaction, the decrease in the energy density due to the decrease in the electrode density can be suppressed, and as a result, the energy density can be improved due to the increase in the electrode density. It is.

(Other ingredients)
Examples of the electrolyte salt (lithium salt) include Li (C ₂ F ₅ SO ₂ ) ₂ N, LiPF ₆ , LiBF ₄ , LiClO ₄ , LiAsF ₆ , LiCF ₃ SO _{3 and the} like.

  Examples of the ion conductive polymer include polyethylene oxide (PEO) -based and polypropylene oxide (PPO) -based polymers.

  The positive electrode (positive electrode active material layer) can be applied by any one of a kneading method, a sputtering method, a vapor deposition method, a CVD method, a PVD method, an ion plating method, and a thermal spraying method in addition to a method of applying (coating) a normal slurry. Can be formed.

[Negative electrode active material layer]
The negative electrode active material layer 15 essentially includes SiO _x and a carbon material as a negative electrode active material.

(SiO _x )
SiO _x is a mixture of amorphous SiO ₂ particles and Si particles, and x represents the number of oxygen satisfying the valence of Si. There is no restriction | limiting in particular about the specific value of x, It can set suitably.

Further, the SiO _x may be an electrically conductive SiO _x particles the surface of the SiO _x particulate is coated with a conductive material by mechanical surface fusion treatment. With such a configuration, Si in the SiO _x particles can easily desorb and insert lithium ions, and the reaction in the active material can proceed more smoothly. In this case, the content of the conductive substance in the conductive SiO _x particles is preferably 1 to 30% by weight, and more preferably 2 to 20% by weight.

The average particle diameter of the SiO _x is not particularly limited as long as it is approximately the same as the average particle diameter of the negative electrode active material contained in the existing negative electrode active material layer 15. From the viewpoint of increasing the output, it is preferably in the range of 1 to 20 μm. However, it is not limited at all to the above range, and it goes without saying that it may be outside the above range as long as the effects of the present embodiment can be effectively expressed. The shape of SiO _x is not particularly limited, and may be spherical, elliptical, cylindrical, polygonal, flaky, indefinite, or the like.

As a method for producing SiO _x in accordance with the manufacturing method according to this embodiment of SiO _x, is not particularly limited, it can be produced by utilizing the production of conventionally known various. That is, since there is almost no difference in the amorphous state / characteristics depending on the manufacturing method, various manufacturing methods can be applied.

The following method is mentioned as a method for preparing SiO _x . First, Si powder and SiO ₂ powder are blended at a predetermined ratio as raw materials, and mixed, granulated and dried mixed granulated raw materials are heated in an inert gas atmosphere (830 ° C. or higher) or heated in vacuum (1 , 100 ° C. or higher and 1,600 ° C. or lower) to generate (sublimate) SiO. Gaseous SiO generated by sublimation is vapor-deposited on the deposition substrate (substrate temperature is 450 ° C. or more and 800 ° C. or less) to deposit SiO precipitates. Thereafter, the SiO _x powder is obtained by removing the SiO deposit from the deposition substrate and pulverizing it using a ball mill or the like.

  The value of x can be determined by fluorescent X-ray analysis. For example, it can be determined using a fundamental parameter method in fluorescent X-ray analysis using O-Kα rays. For the X-ray fluorescence analysis, for example, RIX3000 manufactured by Rigaku Corporation can be used. As conditions for the fluorescent X-ray analysis, for example, rhodium (Rh) may be used as a target, the tube voltage may be 50 kV, and the tube current may be 50 mA. Since the x value obtained here is calculated from the intensity of the O-Kα ray detected in the measurement region on the substrate, it is an average value of the measurement region.

(Carbon material)
The carbon material that can be used in the present invention is not particularly limited, but graphite (graphite), which is a highly crystalline carbon such as natural graphite or artificial graphite; low crystalline carbon such as soft carbon or hard carbon; ketjen black, acetylene Carbon black such as black, channel black, lamp black, oil furnace black, and thermal black; and carbon materials such as fullerene, carbon nanotube, carbon nanofiber, carbon nanohorn, and carbon fibril. Of these, graphite is preferably used.

In the present embodiment, by using a carbon material together with the above SiO _x as the negative electrode active material, it is possible to maintain a high cycle characteristic and rate characteristic and to have a high initial capacity and a well-balanced characteristic.

SiO _x may not be uniformly disposed in the negative electrode active material layer. In such a case, the potential and capacity that each SiO _x develops are different. As a result, in SiO _x of the negative electrode active material layer includes a SiO _x that react excessively lithium ion, SiO _x is produced that does not react with lithium ions. That is, non-uniformity of the reaction between SiO _x and lithium ions in the negative electrode active material layer occurs. Then, SiO _x that reacts with lithium ions excessively acts among the alloys described above, and the decomposition of the electrolytic solution due to a significant reaction with the electrolytic solution or the destruction of the structure of SiO _x due to excessive expansion may occur. As a result, even when SiO _x having excellent characteristics is used, in the case where SiO _x is not uniformly arranged, the cycle characteristics can be deteriorated as a negative electrode for an electric device.

However, when the SiO _x is mixed with a carbon material, the above problem can be solved. More specifically, by mixing SiO _x with a carbon material, it may be possible to uniformly dispose SiO _x in the negative electrode active material layer. As a result, it is considered that any SiO _x in the negative electrode active material layer exhibits the same reactivity and can prevent deterioration of cycle characteristics.

In addition, as a result of mixing the carbon material, the initial capacity can be reduced by reducing the content of SiO _x in the negative electrode active material layer. However, since the carbon material itself has reactivity with lithium ions, the degree of decrease in the initial capacity is relatively small. That is, the negative electrode active material according to the present embodiment has a large effect of improving the cycle characteristics as compared with the effect of reducing the initial capacity.

Further, the carbon material is unlikely to undergo a volume change when reacting with lithium ions as compared with SiO _x . Therefore, even when the volume change of SiO _x is large, when the negative electrode active material is taken as a whole, the influence of the volume change of the negative electrode active material associated with the lithium reaction can be made relatively minor. Such an effect can also be understood from the results of Examples in which the cycle characteristics increase as the carbon material content rate increases (the SiO _x content rate decreases).

Moreover, the amount of electricity consumed (Wh) can be improved by containing a carbon material. More specifically, the carbon material has a relatively low potential compared with SiO _x . As a result, the relatively high potential of SiO _x can be reduced. Then, since the electric potential of the whole negative electrode falls, power consumption (Wh) can be improved. Such an action is particularly advantageous when used in, for example, a vehicle application among electric devices.

  There is no restriction | limiting in particular as a shape of a carbon material, A spherical shape, an ellipse shape, a column shape, a polygonal column shape, a scale shape, an indefinite shape etc. may be sufficient.

The average particle diameter of the carbon material is not particularly limited, but is preferably 5 to 25 μm, and more preferably 5 to 10 μm. At this time, regarding the comparison with the above-mentioned average particle diameter with SiO _x , the average particle diameter of the carbon material may be the same as or different from the average particle diameter of SiO _x , but is preferably different. . In particular, the average particle diameter of the SiO _x is more preferably smaller than the average particle diameter of the carbon material. When the average particle size of the carbon material is relatively larger than the average particle size of SiO _x , the carbon material particles are uniformly arranged, and the SiO _x is arranged between the carbon material particles. SiO _x can be uniformly arranged in the material layer.

The ratio of the average particle diameter of the carbon material to the average particle diameter of SiO _x (the average particle diameter of SiO _x / the average particle diameter of the carbon material) is preferably 1/250 to less than 1, More preferably, it is 100 to 1/4.

Depending on the case, negative electrode active materials other than the two types of negative electrode active materials described above may be used in combination. Examples of the negative electrode active material that can be used in combination include lithium-transition metal composite oxides (for example, Li ₄ Ti ₅ O ₁₂ ), metal materials, lithium alloy negative electrode materials, and the like. Of course, other negative electrode active materials may be used.

  The negative electrode active material layer contains a negative electrode active material represented by the following formula (1).

In the formula (1), SiO _x is a mixture of amorphous SiO ₂ particles and Si particles as described above, and x represents the number of oxygen satisfying the valence of Si. Α (SiO _x ) and β (carbon material) represent weight percentages of SiO _x and carbon material in the negative electrode active material layer, respectively , and 80 ≦ α (SiO _x ) + β (carbon material) ≦ 98, 3 ≦ α ( SiO _x ) ≦ 40, 40 ≦ β (carbon material) ≦ 95.

As apparent from the formula (1), the content of the SiO _x negative electrode active material in the negative electrode active material layer is 3 to 40% by weight. Moreover, content of a carbon material negative electrode active material is 40 to 95 weight%. Furthermore, the total content thereof is 80 to 98% by weight.

In addition, the mixing ratio of SiO _x and the carbon material of the negative electrode active material is not particularly limited as long as the above content specification is satisfied, and can be appropriately selected according to a desired application. Among them, the content of SiO _x of the negative active material in is preferably 3 to 40 wt%. In one embodiment, the content of SiO _x of the negative active material in is more preferably 4 to 30 wt%. Further, in another embodiment, the content of SiO _x of the negative active material in is more preferably 5 to 20 wt%.

It is preferable that the content of SiO _x is 3% by weight or more because a high initial capacity can be obtained. On the other hand, when the content of the SiO _x is 40% by weight or less, it is preferable because high cycle characteristics can be obtained.

  In the present embodiment, the negative electrode active material layer preferably contains a binder and a conductive additive in addition to the negative electrode active material described above. Further, if necessary, it further contains other additives such as an electrolyte (polymer matrix, ion conductive polymer, electrolytic solution, etc.) and a lithium salt for increasing the ion conductivity. About these specific types and preferable contents in the negative electrode active material layer, the above-described embodiments in the column of the description of the positive electrode active material layer can be similarly adopted, and thus detailed description thereof is omitted here.

The present embodiment is characterized in that the coating amount (weight per unit area) of the negative electrode active material layer is 3 to 11 mg / cm ² . When the coating amount (weight per unit area) of the negative electrode active material layer exceeds 11 mg / cm ² , there is a problem that the rate characteristics of the battery are remarkably deteriorated. On the other hand, when the coating amount (weight per unit area) of the negative electrode active material layer is less than 3 mg / cm ² , the content of the active material in the negative electrode active material layer is reduced in the first place, and sufficient capacity cannot be ensured, resulting in cycle durability. It will get worse. On the other hand, if the coating amount (weight per unit area) of the negative electrode active material layer is a value within the above-described range, both rate characteristics and cycle characteristics can be achieved. In the present invention, a predetermined negative electrode active material is used in combination, and the content thereof is adjusted to achieve the coating amount (weight per unit area) within the above range.

  There is no particular limitation on the thickness of each active material layer (active material layer on one side of the current collector), and conventionally known knowledge about the battery can be referred to as appropriate. For example, the thickness of each active material layer is usually about 1 to 500 μm, preferably 2 to 100 μm in consideration of the intended use of the battery (emphasis on output, energy, etc.) and ion conductivity.

<Current collector>
The current collector (11, 12) is made of a conductive material. The size of the current collector is determined according to the intended use of the battery. For example, if it is used for a large battery that requires a high energy density, a current collector having a large area is used.

  There is no particular limitation on the thickness of the current collector. The thickness of the current collector is usually about 1 to 100 μm.

  The shape of the current collector is not particularly limited. In the laminated battery 10 shown in FIG. 1, in addition to the current collector foil, a mesh shape (such as an expanded grid) can be used.

  In the case where the negative electrode active material is formed directly on the negative electrode current collector 12 by sputtering or the like, it is preferable to use a current collector foil.

  There is no particular limitation on the material constituting the current collector. For example, a metal or a resin in which a conductive filler is added to a conductive polymer material or a non-conductive polymer material can be employed.

  Specifically, examples of the metal include aluminum, nickel, iron, stainless steel, titanium, and copper. In addition to these, a clad material of nickel and aluminum, a clad material of copper and aluminum, or a plating material of a combination of these metals can be preferably used. Moreover, the foil by which aluminum is coat | covered on the metal surface may be sufficient. Of these, aluminum, stainless steel, copper, and nickel are preferable from the viewpoints of electronic conductivity, battery operating potential, and adhesion of the negative electrode active material by sputtering to the current collector.

  Examples of the conductive polymer material include polyaniline, polypyrrole, polythiophene, polyacetylene, polyparaphenylene, polyphenylene vinylene, polyacrylonitrile, and polyoxadiazole. Since such a conductive polymer material has sufficient conductivity without adding a conductive filler, it is advantageous in terms of facilitating the manufacturing process or reducing the weight of the current collector.

  Non-conductive polymer materials include, for example, polyethylene (PE; high density polyethylene (HDPE), low density polyethylene (LDPE), etc.), polypropylene (PP), polyethylene terephthalate (PET), polyether nitrile (PEN), polyimide (PI), polyamideimide (PAI), polyamide (PA), polytetrafluoroethylene (PTFE), styrene-butadiene rubber (SBR), polyacrylonitrile (PAN), polymethyl acrylate (PMA), polymethyl methacrylate (PMMA) , Polyvinyl chloride (PVC), polyvinylidene fluoride (PVdF), or polystyrene (PS). Such a non-conductive polymer material may have excellent potential resistance or solvent resistance.

  A conductive filler may be added to the conductive polymer material or the non-conductive polymer material as necessary. In particular, when the resin used as the base material of the current collector is made of only a non-conductive polymer, a conductive filler is inevitably necessary to impart conductivity to the resin.

  The conductive filler can be used without particular limitation as long as it is a substance having conductivity. For example, metals, conductive carbon, etc. are mentioned as a material excellent in electroconductivity, electric potential resistance, or lithium ion barrier | blocking property. The metal is not particularly limited, but at least one metal selected from the group consisting of Ni, Ti, Al, Cu, Pt, Fe, Cr, Sn, Zn, In, Sb, and K, or these metals It is preferable to contain an alloy or metal oxide containing. Moreover, there is no restriction | limiting in particular as electroconductive carbon. Preferably, it includes at least one selected from the group consisting of acetylene black, vulcan, black pearl, carbon nanofiber, ketjen black, carbon nanotube, carbon nanohorn, carbon nanoballoon, and fullerene.

  The amount of the conductive filler added is not particularly limited as long as it is an amount that can impart sufficient conductivity to the current collector, and is generally about 5 to 35% by weight.

<Separator (electrolyte layer)>
The separator has a function of holding an electrolyte and ensuring lithium ion conductivity between the positive electrode and the negative electrode, and a function as a partition wall between the positive electrode and the negative electrode.

  Examples of the separator include a porous sheet separator or a nonwoven fabric separator made of a polymer or fiber that absorbs and holds the electrolyte.

  As a separator for a porous sheet made of a polymer or fiber, for example, a microporous (microporous film) can be used. Specific examples of the porous sheet made of the polymer or fiber include polyolefins such as polyethylene (PE) and polypropylene (PP); a laminate in which a plurality of these are laminated (for example, three layers of PP / PE / PP) And a microporous (microporous membrane) separator made of a hydrocarbon resin such as polyimide, aramid, polyvinylidene fluoride-hexafluoropropylene (PVdF-HFP), glass fiber, and the like.

  The thickness of the microporous (microporous membrane) separator cannot be uniquely defined because it varies depending on the intended use. For example, in applications such as secondary batteries for driving motors such as electric vehicles (EV), hybrid electric vehicles (HEV), and fuel cell vehicles (FCV), it is 4 to 60 μm in a single layer or multiple layers. Is desirable. The fine pore diameter of the microporous (microporous membrane) separator is desirably 1 μm or less (usually a pore diameter of about several tens of nm).

  As the nonwoven fabric separator, cotton, rayon, acetate, nylon, polyester; polyolefins such as PP and PE; conventionally known ones such as polyimide and aramid are used alone or in combination. The bulk density of the nonwoven fabric is not particularly limited as long as sufficient battery characteristics can be obtained by the impregnated polymer gel electrolyte. Furthermore, the thickness of the nonwoven fabric separator may be the same as that of the electrolyte layer, preferably 5 to 200 μm, particularly preferably 10 to 100 μm.

  In addition, as described above, the separator includes an electrolyte. The electrolyte is not particularly limited as long as it can exhibit such a function, but a liquid electrolyte or a gel polymer electrolyte is used. By using the gel polymer electrolyte, the distance between the electrodes is stabilized, the occurrence of polarization is suppressed, and the durability (cycle characteristics) is improved.

The liquid electrolyte functions as a lithium ion carrier. The liquid electrolyte constituting the electrolytic solution layer has a form in which a lithium salt as a supporting salt is dissolved in an organic solvent as a plasticizer. Examples of the organic solvent used include carbonates such as ethylene carbonate (EC), propylene carbonate (PC), dimethyl carbonate (DMC), diethyl carbonate (DEC), and ethyl methyl carbonate. As the lithium _{salt, Li (CF 3 SO 2)} 2 N, Li (C 2 F 5 SO 2) 2 N, LiPF 6, LiBF 4, LiClO 4, LiAsF 6, LiTaF such 6, LiCF ₃ SO ₃ A compound that can be added to the active material layer of the electrode can be similarly employed. The liquid electrolyte may further contain additives other than the components described above. Specific examples of such compounds include, for example, vinylene carbonate, methyl vinylene carbonate, dimethyl vinylene carbonate, phenyl vinylene carbonate, diphenyl vinylene carbonate, ethyl vinylene carbonate, diethyl vinylene carbonate, vinyl ethylene carbonate, 1,2-divinyl ethylene carbonate. 1-methyl-1-vinylethylene carbonate, 1-methyl-2-vinylethylene carbonate, 1-ethyl-1-vinylethylene carbonate, 1-ethyl-2-vinylethylene carbonate, vinylvinylene carbonate, allylethylene carbonate, vinyl Oxymethyl ethylene carbonate, allyloxymethyl ethylene carbonate, acryloxymethyl ethylene carbonate, methacrylate Oxy methylethylene carbonate, ethynyl ethylene carbonate, propargyl carbonate, ethynyloxy methylethylene carbonate, propargyloxy ethylene carbonate, methylene carbonate, etc. 1,1-dimethyl-2-methylene-ethylene carbonate. Among these, vinylene carbonate, methyl vinylene carbonate, and vinyl ethylene carbonate are preferable, and vinylene carbonate and vinyl ethylene carbonate are more preferable. These cyclic carbonates may be used alone or in combination of two or more.

  The gel polymer electrolyte has a configuration in which the liquid electrolyte is injected into a matrix polymer (host polymer) made of an ion conductive polymer. The use of a gel polymer electrolyte as the electrolyte is superior in that the fluidity of the electrolyte is lost and the ion conductivity between the layers is easily cut off. Examples of the ion conductive polymer used as the matrix polymer (host polymer) include polyethylene oxide (PEO), polypropylene oxide (PPO), polyethylene glycol (PEG), polyacrylonitrile (PAN), polyvinylidene fluoride-hexafluoropropylene ( PVdF-HEP), poly (methyl methacrylate (PMMA), and copolymers thereof.

  The matrix polymer of gel electrolyte can express excellent mechanical strength by forming a crosslinked structure. In order to form a crosslinked structure, thermal polymerization, ultraviolet polymerization, radiation polymerization, electron beam polymerization, etc. are performed on a polymerizable polymer (for example, PEO or PPO) for forming a polymer electrolyte using an appropriate polymerization initiator. A polymerization treatment may be performed.

  The separator is preferably a separator (heat-resistant insulating layer-attached separator) in which a heat-resistant insulating layer is laminated on a porous substrate. The heat resistant insulating layer is a ceramic layer containing inorganic particles and a binder. As the separator with a heat-resistant insulating layer, a highly heat-resistant separator having a melting point or a heat softening point of 150 ° C. or higher, preferably 200 ° C. or higher is used. By having the heat-resistant insulating layer, the internal stress of the separator that increases when the temperature rises is relieved, so that the effect of suppressing thermal shrinkage can be obtained. As a result, it is possible to prevent the induction of a short circuit between the electrodes of the battery, so that the battery configuration is unlikely to deteriorate in performance due to a temperature rise. Moreover, by having a heat-resistant insulating layer, the mechanical strength of the separator with a heat-resistant insulating layer is improved, and it is difficult for the separator to break. Furthermore, the separator is less likely to curl in the battery manufacturing process due to the effect of suppressing thermal shrinkage and high mechanical strength.

The inorganic particles in the heat resistant insulating layer contribute to the mechanical strength and heat shrinkage suppressing effect of the heat resistant insulating layer. The material used as the inorganic particles is not particularly limited. Examples thereof include silicon, aluminum, zirconium, titanium oxides (SiO ₂ , Al ₂ O ₃ , ZrO ₂ , TiO ₂ ), hydroxides and nitrides, and composites thereof. These inorganic particles may be derived from mineral resources such as boehmite, zeolite, apatite, kaolin, mullite, spinel, olivine and mica, or may be artificially produced. Moreover, only 1 type may be used individually for these inorganic particles, and 2 or more types may be used together. Of these, silica (SiO ₂ ) or alumina (Al ₂ O ₃ ) is preferably used, and alumina (Al ₂ O ₃ ) is more preferably used from the viewpoint of cost.

The basis weight of the heat-resistant particles is not particularly limited, but is preferably 5 to 15 g / m ² . If it is this range, sufficient ion conductivity will be acquired and it is preferable at the point which maintains heat resistant strength.

  The binder in the heat-resistant insulating layer has a role of bonding the inorganic particles or the inorganic particles and the resin porous substrate layer. By the binder, the heat resistant insulating layer is stably formed, and peeling between the porous substrate layer and the heat resistant insulating layer is prevented.

  The binder used for the heat-resistant insulating layer is not particularly limited. For example, carboxymethyl cellulose (CMC), polyacrylonitrile, cellulose, ethylene-vinyl acetate copolymer, polyvinyl chloride, styrene-butadiene rubber (SBR), isoprene rubber A compound such as butadiene rubber, polyvinylidene fluoride (PVDF), polytetrafluoroethylene (PTFE), polyvinyl fluoride (PVF), or methyl acrylate can be used as the binder. Of these, carboxymethylcellulose (CMC), methyl acrylate, or polyvinylidene fluoride (PVDF) is preferably used. As for these compounds, only 1 type may be used independently and 2 or more types may be used together.

  The binder content in the heat resistant insulating layer is preferably 2 to 20% by weight with respect to 100% by weight of the heat resistant insulating layer. When the binder content is 2% by weight or more, the peel strength between the heat-resistant insulating layer and the porous substrate layer can be increased, and the vibration resistance of the separator can be improved. On the other hand, when the binder content is 20% by weight or less, the gap between the inorganic particles is appropriately maintained, so that sufficient lithium ion conductivity can be ensured.

The thermal contraction rate of the separator with a heat-resistant insulating layer is preferably 10% or less for both MD and TD after holding for 1 hour at 150 ° C. and ² gf / cm ² . By using such a material having high heat resistance, it is possible to effectively prevent the separator from contracting even if the positive electrode heat generation amount increases and the battery internal temperature reaches 150 ° C. As a result, it is possible to prevent the induction of a short circuit between the electrodes of the battery, so that the battery configuration is unlikely to deteriorate in performance due to a temperature rise.

<Current collector plate (tab)>
In a lithium ion secondary battery, a current collector plate (tab) electrically connected to a current collector is taken out of a laminate film as an exterior material for the purpose of taking out current outside the battery.

  The material which comprises a current collector plate is not specifically limited, The well-known highly electroconductive material conventionally used as a current collector plate for lithium ion secondary batteries can be used. As a constituent material of the current collector plate, for example, metal materials such as aluminum, copper, titanium, nickel, stainless steel (SUS), and alloys thereof are preferable. From the viewpoint of light weight, corrosion resistance, and high conductivity, aluminum and copper are more preferable, and aluminum is particularly preferable. Note that the same material may be used for the positive electrode current collector plate (positive electrode tab) and the negative electrode current collector plate (negative electrode tab), or different materials may be used.

  Further, the removal of the tabs 58 and 59 shown in FIG. 2 is not particularly limited. The positive electrode tab 58 and the negative electrode tab 59 may be drawn out from the same side, or the positive electrode tab 58 and the negative electrode tab 59 may be divided into a plurality of parts and taken out from each side, as shown in FIG. It is not limited to. Further, in a wound type lithium ion battery, instead of a tab, for example, a terminal may be formed using a cylindrical can (metal can).

<Seal part>
The seal portion is a member unique to the serially stacked battery and has a function of preventing leakage of the electrolyte layer. In addition to this, it is possible to prevent current collectors adjacent in the battery from coming into contact with each other and a short circuit due to a slight unevenness at the end of the laminated electrode.

  The constituent material of the seal portion is not particularly limited, but polyolefin resin such as polyethylene and polypropylene, epoxy resin, rubber, polyimide and the like can be used. Among these, it is preferable to use a polyolefin resin from the viewpoints of corrosion resistance, chemical resistance, film-forming property, economy, and the like.

<Positive terminal lead and negative terminal lead>
As a material for the negative electrode and the positive electrode terminal lead, a lead used in a known laminated secondary battery can be used. In addition, the parts removed from the battery outer packaging should be heat-insulating so that they do not affect products (for example, automobile parts, especially electronic devices) by touching peripheral devices or wiring and causing leakage. It is preferable to coat with a heat shrinkable tube or the like.

<Exterior material; Laminate film>
A conventionally known metal can case can be used as the exterior material. In addition, the power generation element 21 may be packed using a laminate film 29 as shown in FIG. The laminate film can be configured as a three-layer structure in which, for example, polypropylene, aluminum, and nylon are laminated in this order. By using such a laminate film, it is possible to easily open the exterior material, add the capacity recovery material, and reseal the exterior material.

<Method for producing lithium ion secondary battery>
The manufacturing method in particular of a lithium ion secondary battery is not restrict | limited, It can manufacture by a well-known method. Specifically, it includes (1) production of electrodes, (2) production of single cell layers, (3) production of power generation elements, and (4) production of stacked batteries. Hereinafter, although an example is given and demonstrated about the manufacturing method of a lithium ion secondary battery, it is not limited to this.

(1) Production of electrodes (positive electrode and negative electrode) The electrode (positive electrode or negative electrode) is prepared, for example, by preparing an active material slurry (positive electrode active material slurry or negative electrode active material slurry) and applying the active material slurry onto a current collector. It can be made by drying, then pressing. The active material slurry includes the above-described active material (positive electrode active material or negative electrode active material), a binder, a conductive additive, and a solvent.

  The solvent is not particularly limited, and N-methyl-2-pyrrolidone (NMP), dimethylformamide, dimethylacetamide, methylformamide, cyclohexane, hexane, water and the like can be used.

  A method for applying the active material slurry to the current collector is not particularly limited, and examples thereof include a screen printing method, a spray coating method, an electrostatic spray coating method, an ink jet method, and a doctor blade method.

  The method for drying the coating film formed on the surface of the current collector is not particularly limited as long as at least a part of the solvent in the coating film is removed. An example of the drying method is heating. Drying conditions (drying time, drying temperature, etc.) can be appropriately set according to the volatilization rate of the solvent contained in the applied active material slurry, the coating amount of the active material slurry, and the like. A part of the solvent may remain. The remaining solvent can be removed by a press process described later.

  The pressing means is not particularly limited, and for example, a calendar roll, a flat plate press or the like can be used.

(2) Production of single cell layer The single cell layer can be produced by laminating the electrodes (positive electrode and negative electrode) produced in (1) via an electrolyte layer.

(3) Production of power generation element The power generation element can be produced by laminating the single cell layers in consideration of the output and capacity of the single cell layer, the output and capacity required for the battery, and the like.

(4) Manufacture of laminated battery As the structure of the battery, various shapes such as a rectangular shape, a paper shape, a laminated shape, a cylindrical shape, and a coin shape can be adopted. Further, the current collector and insulating plate of the component parts are not particularly limited, and may be selected according to the above shape. However, in the present embodiment, a stacked battery is preferable. In the stacked battery, a lead is joined to the current collector of the power generation element obtained above, and the positive electrode lead or the negative electrode lead is joined to the positive electrode tab or the negative electrode tab. A power generation element is placed in a laminate sheet so that the positive electrode tab and the negative electrode tab are exposed to the outside of the battery, and an electrolytic solution is injected by a liquid injector and then sealed in a vacuum to produce a stacked battery. sell.

(5) Activation treatment, etc. Further, in this embodiment, from the viewpoint of enhancing the performance and durability of the laminated battery obtained as described above, the initial charge treatment, gas removal treatment and activation treatment are further performed under the following conditions. Preferably it is done (see Example 1). In this case, the three sides of the laminate sheet (exterior material) are completely sealed in a rectangular shape by thermocompression when sealing in the production of the laminated battery of (4) so that the gas removal treatment can be performed. Stop (main sealing), and the remaining one side is temporarily sealed by thermocompression bonding. The remaining one side may be freely opened and closed by, for example, clip fastening, but from the viewpoint of mass production (production efficiency), it is preferable to temporarily seal the side by thermocompression bonding. In this case, it is only necessary to adjust the temperature and pressure for pressure bonding. When temporarily sealed by thermocompression, it can be opened by lightly applying force, and after degassing, it may be sealed again by thermocompression, or finally completely sealed by thermocompression ( Main sealing).

(First charging process)
The battery aging treatment is preferably performed as follows. At 25 ° C., a constant current charging method is used for 0.05 C for 4 hours (SOC approximately 20%). Next, after charging to 4.45 V at a 0.1 C rate at 25 ° C., the charging is stopped, and the state (SOC is about 70%) is maintained for about 2 days (48 hours).

(First (first) gas removal process)
Next, the following process is performed as the first (first) gas removal process. First, one side temporarily sealed by thermocompression bonding is opened, gas is removed at 10 ± 3 hPa for 5 minutes, and then thermocompression bonding is performed again to perform temporary sealing. Further, pressurization with a roller (surface pressure 0.5 ± 0.1 MPa) is performed, and the electrode and the separator are sufficiently adhered.

(Activation process)
Next, the following electrochemical pretreatment method is performed as an activation treatment method.

  First, the battery is charged at 25 ° C. by a constant current charging method until the voltage reaches 4.45 V at 0.1 C, and then discharged twice to 2.0 V at 0.1 C. Similarly, after charging at 25 ° C. to 4.55 V at 0.1 C by the constant current charging method, a cycle of discharging to 2.0 V at 0.1 C once is 4.65 V at 0.1 C. The battery is charged until it reaches 0, and then discharged once at 0.1 C to 2.0 V. Furthermore, a cycle of charging at 0.1 C to 4.75 V by a constant current charging method at 25 ° C. and then discharging to 0.1 V at 0.1 C may be performed once.

  In this example, the constant current charging method is used as the activation processing method, and the electrochemical pretreatment method when the voltage is set as the termination condition is described as an example, but the charging method is a constant current constant voltage charging method. You may use. Further, as the termination condition, a charge amount or time may be used in addition to the voltage.

(Last (second) gas removal process)
Next, the following process is performed as the last ( second ) gas removal process. First, one side temporarily sealed by thermocompression bonding is opened, gas is removed at 10 ± 3 hPa for 5 minutes, and then thermocompression bonding is performed again to perform main sealing. Further, pressurization with a roller (surface pressure 0.5 ± 0.1 MPa) is performed, and the electrode and the separator are sufficiently adhered.

  In the present embodiment, the performance and durability of the obtained battery can be enhanced by performing the initial charging process, the gas removal process, and the activation process described above.

[Battery]
The assembled battery is configured by connecting a plurality of batteries. Specifically, at least two or more are used, and are configured by serialization, parallelization, or both. Capacitance and voltage can be freely adjusted by paralleling in series.

  A plurality of batteries can be connected in series or in parallel to form a small assembled battery that can be attached and detached. Then, a plurality of small assembled batteries that can be attached and detached are connected in series or in parallel to provide a large capacity and large capacity suitable for vehicle drive power supplies and auxiliary power supplies that require high volume energy density and high volume output density. An assembled battery having an output can also be formed. How many batteries are connected to make an assembled battery, and how many small assembled batteries are stacked to make a large-capacity assembled battery depends on the battery capacity of the mounted vehicle (electric vehicle) It may be determined according to the output.

[vehicle]
The electric device of the present invention including the lithium ion secondary battery according to the present embodiment maintains a discharge capacity even when used for a long period of time, and has good cycle characteristics. Furthermore, the volume energy density is high. Vehicle applications such as electric vehicles, hybrid electric vehicles, fuel cell vehicles, and hybrid fuel cell vehicles require higher capacity, larger size, and longer life than electric and portable electronic devices. . Therefore, the lithium ion secondary battery (electric device) can be suitably used as a vehicle power source, for example, as a vehicle driving power source or an auxiliary power source.

  Specifically, a battery or an assembled battery formed by combining a plurality of these batteries can be mounted on a vehicle. In the present invention, since a battery having a long life with excellent long-term reliability and output characteristics can be configured, a plug-in hybrid electric vehicle having a long EV mileage or an electric vehicle having a long charge mileage can be formed by mounting such a battery. . For example, in the case of a car, a hybrid car, a fuel cell car, an electric car (four-wheeled vehicles (passenger cars, trucks, buses, commercial vehicles, light cars, etc.) This is because it can be used for motorcycles (including motorcycles) and tricycles) to provide a long-life and highly reliable automobile. However, the application is not limited to automobiles. For example, it can be applied to various power sources for moving vehicles such as other vehicles, for example, trains, and power sources for mounting such as uninterruptible power supplies. It is also possible to use as.

  Hereinafter, although it demonstrates still in detail using an Example and a comparative example, this invention is not necessarily limited to the following Examples at all.

[Example 1]
(Solid solution positive electrode active material C1)
(Preparation of aqueous solution of titanium citrate complex)
60 g (0.3 mol) of anhydrous citric acid (molecular weight 192.12 g / mol) was added to 400 ml of acetone and heated to 60 ° C. to dissolve. Next, 56 g (0.2 mol) of titanium tetraisopropoxide (molecular weight 284.22 g / mol) was added to form a precipitate. This liquid was subjected to suction filtration to obtain a precipitate (light yellow).

H ₂ O (200 ml) was added to the precipitate and heated to 50 to 60 ° C. to dissolve. This solution was allowed to stand for 1 day or longer to precipitate insoluble matters, and then filtered to remove insoluble matters, thereby obtaining a titanium citrate complex aqueous solution. The Ti concentration was 5.0% by weight as TiO ₂ (molecular weight 79.87 g / mol).

(Preparation of solid solution positive electrode active material C1)
Li _1.5 [Ni _0.450 Mn _0.750 [Li] _0.20 Ti _0.10 ] O _z
15.97 g of titanium citrate complex aqueous solution (5.0 wt% as TiO ₂ ), 14.71 g of manganese acetate tetrahydrate (molecular weight 245.09 g / mol), nickel acetate tetrahydrate (molecular weight 248. 84 g / mol) 7.47 g and lithium acetate dihydrate (molecular weight 102.02 g / mol) 14.57 g were sequentially added. The obtained mixture was heated to 200 ° C. to 300 ° C. and melted and dissolved. Next, the obtained melt solution (slurry) was sprayed by heating at 200 ° C. to 400 ° C. using a spray drying apparatus and dried. The obtained dry powder was vacuum-dried at 140 ° C. to 250 ° C. for 12 hours and then calcined at 450 ° C. for 12 hours. Thereafter, the main baking was performed at 900 ° C. for 12 hours.

The composition of the solid solution positive electrode active material C1 obtained as described above was as follows.
Composition formula: Li _1.5 [Ni _0.450 Mn _0.750 [Li] _0.20 Ti _0.10 ] O _z
a + b + c + d + e = 1.5, d = 0.20, a + b + c + e = 1.30, e = 0.10
(X-ray diffraction measurement)
The obtained solid solution positive electrode active material was evaluated for crystal structure and crystallinity by X-ray diffraction. Cu-Kα rays were used as the X-ray source, and the measurement conditions were a tube voltage of 40 KV, a tube current of 20 mA, a scanning speed of 2 ° / min, a divergence slit width of 0.5 °, and a light receiving slit width of 0.15 °.

FIG. 3 shows a positive electrode active material C0 having the following composition that does not contain Ti for comparison.
Composition formula: Li _1.5 [Ni _0.450 Mn _0.850 [Li] _0.20 Ti _0.00 ] O _z
The X-ray diffraction pattern of is shown. Further, FIG. 4 shows an X-ray diffraction pattern of the solid solution positive electrode active material C1.

  In FIGS. 3 and 4, a peak attributed to the superlattice structure characteristic of the solid solution system is observed at 20-23 °. Furthermore, in FIG. 4, the peaks at 36.5-37.5 (101) and 44-45 ° (104) and 64-65 ° (108) / 65-66 (110) are slightly shifted to the lower angle side. It was observed. Further, no diffraction peak attributed to the spinel phase was observed in any sample.

(Preparation of positive electrode C1 having a positive electrode active material layer formed on one side of a current collector)
(Composition of slurry for positive electrode)
The positive electrode slurry had the following composition.

Cathode active material: Ti substituted solid solution cathode active material C1 obtained above 9.4 parts by weight Conductive aid: flake graphite 0.15 parts by weight
0.15 parts by weight of acetylene black Binder: 0.3 parts by weight of polyvinylidene fluoride (PVDF) Solvent: 8.2 parts by weight of N-methyl-2-pyrrolidone (NMP)

When this composition is applied to the formula (2), f (solid solution positive electrode active material) = 94, which satisfies the requirement of the formula (2).

(Production of positive electrode slurry)
A positive electrode slurry having the above composition was prepared as follows. First, 4.0 parts by weight of a solvent (NMP) is added to 2.0 parts by weight of a 20% binder solution obtained by dissolving a binder in a solvent (NMP) into a 50 ml disposable cup, and a stirring defoaming machine (spinning revolving mixer: Awatori) A diluted binder solution was prepared by stirring for 1 minute with Rentaro AR-100). Next, 0.4 parts by weight of a conductive additive, 9.2 parts by weight of a solid solution positive electrode active material C1, and 2.6 parts by weight of a solvent (NMP) are added to the binder dilution, and the mixture is stirred for 3 minutes with a stirring deaerator. Thus, a positive electrode slurry (solid content concentration 55% by weight) was obtained.

(Application and drying of positive electrode slurry)
The positive electrode slurry was applied to one side of an aluminum current collector with a thickness of 20 μm using an automatic coating apparatus (Doctor blade manufactured by Tester Sangyo: PI-1210 automatic coating apparatus). Subsequently, the current collector coated with the positive electrode slurry was dried on a hot plate (100 ° C. to 110 ° C., drying time 30 minutes), and the amount of NMP remaining in the positive electrode active material layer was 0.02 wt%. A sheet-like positive electrode was formed as follows.

(Positive electrode press)
The sheet-like positive electrode was compression-molded by applying a roller press and cut to prepare a positive electrode having a weight of about 17.0 mg / cm ² and a density of 2.65 g / cm ³ of the positive electrode active material layer on one side.

(Dry cathode)
Next, the drying process was performed in the vacuum drying furnace using the positive electrode produced in the said procedure. After the positive electrode was installed inside the drying furnace, the pressure in the room was reduced (100 mmHg (1.33 × 10 ⁴ Pa)) at room temperature (25 ° C.) to remove the air in the drying furnace. Subsequently, while flowing nitrogen gas (100 cm ³ / min), the temperature was raised to 120 ° C. at 10 ° C./min, the pressure was reduced again at 120 ° C., and nitrogen was maintained in the furnace for 12 hours. The temperature was lowered. In this way, a positive electrode C1 from which moisture on the positive electrode surface was removed was obtained.

(Preparation of negative electrode A1 in which an active material layer is formed on one side of the current collector foil)
(Composition of slurry for negative electrode)
The negative electrode slurry had the following composition.

Negative electrode active material: SiO _x (Kusaka rare metal, x = 1) 1.00 parts by weight
Carbon material (manufactured by Hitachi Chemical, graphite) 8.45 parts by weight Conductive aid: SuperP 0.20 part by weight Binder: 0.35 parts by weight of polyvinylidene fluoride (PVDF) Solvent: N-methyl-2-pyrrolidone (NMP) 10 0.0 parts by weight.

When this composition is applied to the formula (1), α (SiO _x ) + β (carbon material) = 94.5, α (SiO _x ) = 10, β (carbon material) = 84.5. Satisfy requirements. The average particle size of the carbon material was 24 μm, and the average particle size of SiO _x was 0.5 μm.

(Manufacture of negative electrode slurry)
A negative electrode slurry having the above composition was prepared as follows. First, 5 parts by weight of a solvent (NMP) was added to 1.75 parts by weight of a 20% binder solution obtained by dissolving a binder in a solvent (NMP), and the mixture was stirred for 1 minute with a stirring deaerator to prepare a binder diluted solution. To this binder diluted solution, 0.2 parts by weight of conductive auxiliary agent, 9.45 parts by weight of negative electrode active material powder, and 3.6 parts by weight of solvent (NMP) are added, and the mixture is stirred for 3 minutes with a stirring defoaming machine. A slurry (solid content concentration 50 wt%) was obtained.

(Application and drying of slurry for negative electrode)
The negative electrode slurry was applied to one side of a 10 μm thick electrolytic copper current collector using an automatic coating apparatus. Subsequently, the current collector coated with the negative electrode slurry was dried on a hot plate (100 ° C. to 110 ° C., drying time 30 minutes), and the amount of NMP remaining in the negative electrode active material layer was 0.02% by weight or less. A sheet-like negative electrode was formed.

(Negative electrode press)
The obtained sheet-like negative electrode was compression-molded by a roller press and cut to prepare a negative electrode having a weight of about 8.54 mg / cm ² and a density of 1.45 g / cm ³ of the negative electrode active material layer on one side. When the surface of this negative electrode was observed, no cracks were observed.

(Dry electrode)
Next, the drying process was performed in the vacuum drying furnace using the negative electrode produced in the said procedure. After installing the negative electrode inside the drying furnace, the air in the drying furnace was removed under reduced pressure (100 mmHg (1.33 × 10 ⁴ Pa)) at room temperature (25 ° C.). Subsequently, while flowing nitrogen gas (100 cm ³ / min), the temperature was raised to 135 ° C. at 10 ° C./min, the pressure was reduced again at 135 ° C., and the nitrogen in the furnace was kept exhausted for 12 hours, The temperature was lowered. In this way, moisture on the surface of the negative electrode was removed to obtain a negative electrode A1.

[Capacity confirmation of positive electrode C1]
[Production of coin cell]
The positive electrode C1 obtained by the above (punching to a diameter of 15 mm) and a counter electrode made of a lithium foil (Honjo Metal Co., Ltd., diameter 16 mm, thickness 200 μm) are passed through a separator (diameter 17 mm, Cellguard Cellguard 2400). After facing each other, an electrolytic solution was injected to produce a CR2032-type coin cell.

As the above electrolyte solution, ethylene carbonate (EC) and diethyl carbonate (DEC) 1: in a mixed nonaqueous solvent were mixed at a volume ratio, the concentration of LiPF ₆ a (lithium hexafluorophosphate) 1M What was dissolved so that it might become was used.

  Using a charge / discharge tester (HJ0501SM8A manufactured by Hokuto Denko Co., Ltd.), activation treatment and performance evaluation were performed in a thermostatic chamber (PFU-3K manufactured by Espec Co., Ltd.) set at a temperature of 298K (25 ° C). .

[Activation processing]
After charging at 25 ° C. by a constant current charging method at 0.1 C until the voltage reached 4.45 V, a cycle of discharging to 0.1 V at 0.1 C was performed twice. Similarly, after charging at 25 ° C. to 4.55 V at 0.1 C by the constant current charging method, a cycle of discharging to 2.0 V at 0.1 C once is 4.65 V at 0.1 C. After being charged until it was, a cycle of discharging to 2.0 V at 0.1 C was performed once. Furthermore, the battery was charged at 25 ° C. by a constant current charging method until it reached 4.75 V at 0.1 C, and then discharged once to 2.0 V at 0.1 C.

[Performance evaluation]
The battery is evaluated by a constant current / constant voltage charging method in which charging is performed at a rate of 0.1 C until the maximum voltage reaches 4.5 V, and then held for about 1 hour to 1.5 hours. The constant current discharge method was used in which discharge was performed at a 0.1 C rate until the minimum voltage reached 2.0V. The discharge capacity at the 0.1 C rate at this time was defined as “0.1 C discharge capacity (mAh / g)”.

As a result, the discharge capacity per active material of the positive electrode C1 was 221 mAh / g, and the discharge capacity per electrode unit area was 3.61 mAh / cm ² .

[Confirmation of capacity of negative electrode A1]
[Production of coin cell]
The negative electrode A1 obtained by the above (punching to a diameter of 15 mm) and a counter electrode made of lithium foil (Honjo Metal Co., Ltd., diameter: 16 mm, thickness: 200 μm) were passed through a separator (diameter: 17 mm, Celgard Cellguard 2400). After facing each other, an electrolytic solution was injected to produce a CR2032-type coin cell.

As the above electrolyte solution, ethylene carbonate (EC) and diethyl carbonate (DEC) 1: in a mixed nonaqueous solvent were mixed at a volume ratio, the concentration of LiPF ₆ a (lithium hexafluorophosphate) 1M What was dissolved so that it might become was used.

  Using a charge / discharge tester (HJ0501SM8A manufactured by Hokuto Denko Co., Ltd.), performance evaluation was performed in a thermostatic chamber (PFU-3K manufactured by Espec Co., Ltd.) set at a temperature of 298K (25 ° C.).

[Performance evaluation]
The battery is evaluated by a constant current constant voltage charging method in which charging (a process of inserting Li into the negative electrode to be evaluated) is charged from 2 V to 10 mV at a rate of 0.1 C and then held for about 1 to 1.5 hours. In the discharge process (the Li desorption process from the negative electrode), the constant current mode was used, and a constant current discharge method was performed in which discharge was performed from 10 mV to 2 V at a 0.1 C rate. The discharge capacity at the 0.1 C rate at this time was defined as “0.1 C discharge capacity (mAh / g)”.

As a result, the discharge capacity per active material (carbon material) of the negative electrode A1 was 363 mAh / g, and the discharge capacity per active material (SiO _x ) was 1,700 mAh / g. Therefore, the discharge capacity per active material of the negative electrode A1 was 505 mAh / g, and the discharge capacity per electrode unit area was 4.08 mAh / cm ² .

[Production of laminate cell]
The positive electrode C1 obtained above was cut out so as to have an active material layer area of 2.5 cm in length and 2.0 cm in width, and the two current collectors faced each other, so that the uncoated surface (aluminum current collector) The current collector portion was spot welded together with the surface not coated with the foil slurry. This formed the positive electrode which has a positive electrode active material layer on both surfaces of the two-ply current collector foil with which the outer peripheral part was integrated by spot welding. Thereafter, an aluminum positive electrode tab (positive electrode current collector plate) was further welded to the current collector portion to form a positive electrode C11. That is, the positive electrode C11 has a configuration in which a positive electrode active material layer is formed on both surfaces of the current collector foil.

  On the other hand, the negative electrode A1 obtained above was cut out so as to have an active material layer area of 2.7 cm in length and 2.2 cm in width, and then a negative electrode tab of electrolytic copper was further welded to the current collector portion to form a negative electrode A11. Formed. That is, the negative electrode A11 has a structure in which a negative electrode active material layer is formed on one surface of a current collector.

A porous polypropylene separator (S) (length 3.0 cm × width 2.5 cm, thickness 25 μm, porosity 55%) is sandwiched between the negative electrode A11 to which these tabs are welded and the positive electrode C11. A laminated power generation element was produced. The structure of the laminated power generation element was laminated in the order of negative electrode (single side) / separator / positive electrode (both sides) / separator / negative electrode (single side), that is, A11- (S) -C11- (S) -A11. The configuration. Next, both sides of the power generation element were sandwiched with an aluminum laminate film exterior material (length 3.5 cm × width 3.5 cm), and the above power generation element was accommodated by thermocompression sealing at three sides. After injecting an electrolyte solution of 0.8 cm ³ into this power generation element (in the case of the above five-layer structure, it becomes a two-cell structure and the amount of liquid injected per cell is 0.4 cm ³ ), the remaining one side is subjected to thermocompression bonding. Was temporarily sealed to prepare a laminated battery. In order to sufficiently infiltrate the electrolyte into the electrode pores, the electrolyte was held at 25 ° C. for 24 hours while being pressurized at a surface pressure of 0.5 Mpa.

In the preparation of the electrolytic solution, first, 1.0 M LiPF ₆ (electrolyte) was dissolved in a mixed solvent of 30% by volume of ethylene carbonate (EC) and 70% by volume of diethyl carbonate (DEC). Thereafter, lithium lithium fluorophosphate (LiPO ₂ F ₂ ) 1.8% by weight and methylenemethane disulfonic acid (MMDS) 1.5% by weight as lithium fluorophosphate acting as an additive were dissolved in an electrolytic solution. Used as.

  In the following examples, active materials were prepared according to Example 1. That is, an active material was prepared in the same manner as in Example 1 described above, except as otherwise noted below.

(Solid solution positive electrode active material C2)
In accordance with Example 1, to prepare a solid solution positive electrode active material _{C2 Li 1.5 [Ni 0.525 Mn 0.725} [Li] 0.15 Ti 0.10] O 3. When the composition of the solid solution positive electrode active material C2 is applied to the formula (3), a + b + c + d = 1.5, d = 0.15, a + b + c + e = 1.35, e = 0.10, which satisfies the requirement of the formula (3). .

(Solid solution positive electrode active material C3)
In accordance with Example 1, to prepare a solid solution positive electrode active material _{C3 Li 1.5 [Ni 0.375 Mn 0.775} [Li] 0.25 Ti 0.10] O 3. When the composition of the solid solution positive electrode active material C3 is applied to the formula (3), a + b + c + d + e = 1.5, d = 0.25, a + b + c + e = 1.25, e = 0.10, which satisfies the requirement of the formula (3). .

(Solid solution positive electrode active material C4)
A solid solution positive electrode active material C4 Li _1.5 [Ni _0.600 Mn _0.700 [Li] _0.10 Ti _0.10 ] O ₃ was produced according to Example 1. When the composition of the solid solution positive electrode active material C4 is applied to the formula (3), a + b + c + d + e = 1.5, d = 0.10, a + b + c + e = 1.40, e = 0.10, which satisfies the requirement of the formula (3). .

(Solid solution positive electrode active material C5)
A solid solution positive electrode active material C5 Li _1.5 [Ni _0.300 Mn _0.800 [Li] _0.30 Ti _0.10 ] O ₃ was produced according to Example 1. When the composition of the solid solution positive electrode active material C5 is applied to the formula (3), a + b + c + d + e = 1.5, d = 0.30, a + b + c + e = 1.20, e = 0.10, which satisfies the requirement of the formula (3). .

(Solid solution positive electrode active material C6)
A solid solution positive electrode active material C6 Li _1.5 [Ni _0.225 Mn _0.825 [Li] _0.35 Ti _0.10 ] O ₃ was produced according to Example 1. When the composition of the solid solution positive electrode active material C6 is applied to the formula (3), a + b + c + d + e = 1.5, d = 0.35, a + b + c + e = 1.15, e = 0.10, which satisfies the requirement of the formula (3). .

(Solid solution positive electrode active material C7)
In accordance with Example 1, to prepare a solid solution positive electrode active material _{C7 Li 1.5 [Ni 0.450 Mn 0.800} [Li] 0.20 Ti 0.05] O 3. When the composition of the solid solution positive electrode active material C7 is applied to the formula (3), a + b + c + d + e = 1.5, d = 0.20, a + b + c + e = 1.30, e = 0.05, which satisfies the requirement of the formula (3). .

(Solid solution positive electrode active material C8)
In accordance with Example 1, to prepare a solid solution positive electrode active material _{C8 Li 1.5 [Ni 0.450 Mn 0.650} [Li] 0.20 Ti 0.20] O 3. When the composition of the solid solution positive electrode active material C7 is applied to the formula (3), a + b + c + d + e = 1.5, d = 0.20, a + b + c + e = 1.30, e = 0.20, which satisfies the requirement of the formula (3). .

(Solid solution positive electrode active material C9)
(Preparation of zirconium citrate complex aqueous solution)
60 g (0.3 mol) of anhydrous citric acid (molecular weight 192.12 g / mol) was added to 400 ml of acetone and heated to 60 ° C. to dissolve. Subsequently, 77.53 g (0.2 mol) of zirconium tetraisopropoxide (molecular weight 387.67 g / mol) was added to form a precipitate. This liquid was subjected to suction filtration to obtain a precipitate (light yellow). H ₂ O (200 ml) was added to the precipitate and heated to 50 to 60 ° C. to dissolve. The obtained solution was allowed to stand for 1 day or longer to precipitate the insoluble matter, and then filtered to remove the insoluble matter to obtain a zirconium citrate complex aqueous solution. The Zr concentration was 5.0% by weight as ZrO ₂ .

(Preparation of solid solution positive electrode active material C9)
The solid solution positive electrode active material C9 Li _1.5 [Ni _0.450 Mn _0.800 [Li] was used according to Example 1 except that the aqueous solution of zirconium citrate complex prepared above was used instead of the aqueous solution of titanium citrate complex. ] _0.20 Zr _0.05 ] Oz was produced. When the composition of the solid solution positive electrode active material C9 is applied to the formula (3), a + b + c + d + e = 1.5, d = 0.20, a + b + c + e = 1.30, e = 0.05, which satisfies the requirement of the formula (3). .

(Solid solution positive electrode active material C10)
A solid solution positive electrode active material C10 Li _1.5 [Ni _0.450 Mn _0.750 [Li] _0.20 Zr _0.10 ] O ₃ was prepared according to Example 9. When the composition of the solid solution positive electrode active material C10 is applied to the formula (3), a + b + c + d + e = 1.5, d = 0.20, a + b + c + e = 1.30, e = 0.10, which satisfies the requirement of the formula (3). .

(Solid solution positive electrode active material C11)
(Preparation of niobium citrate complex aqueous solution)
60 g (0.3 mol) of anhydrous citric acid (molecular weight 192.12 g / mol) was added to 400 ml of acetone and heated to 60 ° C. to dissolve. Next, 63.64 g (0.2 mol) of niobium pentaethoxide (molecular weight 318.21 g / mol) was added to form a precipitate. This liquid was subjected to suction filtration to obtain a precipitate (light yellow). H ₂ O (200 ml) was added to the resulting precipitate, and the mixture was heated to 50-60 ° C. and dissolved. The obtained solution was allowed to stand for 1 day or longer to precipitate the insoluble matter, and then filtered to remove the insoluble matter to obtain a niobium citrate complex aqueous solution. The Nb concentration was 5.0% by weight as Nb ₂ O ₅ .

(Preparation of solid solution positive electrode active material C11)
The solid solution positive electrode active material C11 Li _1.5 [Ni _0.450 Mn _0.825 [Li] was used according to Example 1 except that the niobium citrate complex aqueous solution prepared above was used instead of the titanium citrate complex aqueous solution. _0.20 Nb _0.025 ] Oz was prepared. When the composition of the solid solution positive electrode active material C9 is applied to the formula (3), a + b + c + d + e = 1.5, d = 0.20, a + b + c + e = 1.30, e = 0.025, which satisfies the requirement of the formula (3). .

(Solid solution positive electrode active material C12)
A solid solution positive electrode active material C12 Li _1.5 [Ni _0.450 Mn _0.800 [Li] _0.20 Nb _0.05 ] O ₃ was prepared according to Example 11. When the composition of the solid solution positive electrode active material C10 is applied to the formula (3), a + b + c + d + e = 1.5, d = 0.20, a + b + c + e = 1.30, e = 0.05, which satisfies the requirement of the formula (3). .

(Solid solution positive electrode active material C13)
A solid solution positive electrode active material Li _1.5 [Ni _0.45 Mn _0.85 [Li] _0.20 ] O _{3 in} which Mn is not substituted by another metal was used as the solid solution positive electrode active material C13.

According to Example 1, positive electrodes C2 to C13 were prepared using the solid solution positive electrode active materials C2 to C13 prepared above, respectively. At this time, the coating amount was adjusted in consideration of the discharge capacity of the solid solution positive electrode active material and the positive electrode slurry composition so that the discharge capacities of the positive electrodes C2 to C13 were 3.61 mAh / cm ² . The composition of the positive electrodes C1 to C13 obtained and the measured values of the charge capacity and the discharge capacity are summarized in Table 1 below.

(Negative electrode A2)
A negative electrode A2 was produced in the same manner as in Example 1 except that the composition of the negative electrode slurry was as follows.

Negative electrode active material: 0.47 parts by weight of SiO _x
Carbon material 8.98 parts by weight Conductive aid: SuperP 0.20 parts by weight Binder: Polyvinylidene fluoride (PVDF) 0.35 parts by weight Solvent: N-methyl-2-pyrrolidone (NMP) 10.0 parts by weight.

When this composition is applied to the formula (1), α (SiO _x ) + β (carbon material) = 94.5, α (SiO _x ) = 4.7, β (carbon material) = 89.8, and the formula (1 ) Satisfy the requirements. Moreover, the weight of the negative electrode active material layer on one side of the negative electrode A2 was 10.35 mg / cm ² , and the density was 1.45 g / cm ³ .

(Negative electrode A3)
A negative electrode A3 was produced in the same manner as in Example 1 except that the composition of the negative electrode slurry was as follows.

Negative electrode active material: 2.00 parts by weight of SiO _x
7.10 parts by weight of carbon material Conductive aid: 0.40 part by weight of SuperP Binder: 0.50 part by weight of polyvinylidene fluoride (PVDF) Solvent: 10.0 parts by weight of N-methyl-2-pyrrolidone (NMP)

When this composition is applied to the formula (1), α (SiO _x ) + β (carbon material) = 91.0, α (SiO _x ) = 20.0, β (carbon material) = 71.0. ) Satisfy the requirements. Moreover, the weight of the negative electrode active material layer on one side of the negative electrode A3 was 6.31 mg / cm ² , and the density was 1.45 g / cm ³ .

(Negative electrode A4)
A negative electrode A4 was produced in the same manner as in Example 1 except that the composition of the negative electrode slurry was as follows.

Negative electrode active material: SiO _x 3.00 parts by weight
5.80 parts by weight of carbon material Conductive aid: 0.60 parts by weight of SuperP Binder: 0.60 parts by weight of polyvinylidene fluoride (PVDF) Solvent: 10.0 parts by weight of N-methyl-2-pyrrolidone (NMP)

When this composition is applied to the formula (1), α (SiO _x ) + β (carbon material) = 88.0, α (SiO _x ) = 30.0, β (carbon material) = 58.0, and the formula (1 ) Satisfy the requirements. The weight of the negative electrode active material layer on one side of the negative electrode A4 was 4.94 mg / cm ² , and the density was 1.45 g / cm ³ .

(Negative electrode A5)
9.5 g of the negative electrode active material SiO _x used in Example 1 and 0.5 g of the conductive auxiliary agent SuperP were mixed and subjected to mechanical surface fusion treatment by a mechanical alloy method, whereby the surface was made conductive with SiO _x particles as a nucleus. Conductive SiO _x particles coated with a conductive material (SuperP). The content of the conductive substance in the conductive SiO _x particles was 5% by weight.

  A negative electrode A5 was produced in the same manner as in Example 1 except that the composition of the negative electrode slurry was as follows.

Negative electrode active material: 1.06 parts by weight of conductive SiO _x particles
8.45 parts by weight of carbon material Conductive aid: 0.15 parts by weight of SuperP Binder: 0.35 parts by weight of polyvinylidene fluoride (PVDF) Solvent: 10.0 parts by weight of N-methyl-2-pyrrolidone (NMP).

When this composition is applied to the formula (1), α (SiO _x ) + β (carbon material) = 94.5, α (SiO _x ) = 10.0, β (carbon material) = 84.5, and the formula (1 ) Satisfy the requirements. Moreover, the weight of the negative electrode active material layer on one side of the negative electrode A5 was 8.54 mg / cm ² , and the density was 1.45 g / cm ³ .

(Negative electrode A6)
By mixing 9.0 g of the negative electrode active material SiO _x used in Example 1 and 1.0 g of the conductive auxiliary agent SuperP, and performing a mechanical surface fusion treatment by a mechanical alloy method, the surface is made conductive using SiO _x particles as a nucleus. Conductive SiO _x particles coated with a conductive material (SuperP). The content of the conductive substance in the conductive SiO _x particles was 10% by weight.

  A negative electrode A6 was produced in the same manner as in Example 1 except that the composition of the negative electrode slurry was as follows.

Negative electrode active material: 1.11 parts by weight of conductive SiO _x
Carbon material 8.45 parts by weight Conductive aid: SuperP 0.09 parts by weight Binder: Polyvinylidene fluoride (PVDF) 0.35 parts by weight Solvent: N-methyl-2-pyrrolidone (NMP) 10.0 parts by weight.

When this composition is applied to the formula (1), α (SiO _x ) + β (carbon material) = 95.6, α (SiO _x ) = 11.1, β (carbon material) = 84.5. ) Satisfy the requirements. The weight of the negative electrode active material layer on one side of the negative electrode A6 was 8.54 mg / cm ² , and the density was 1.45 g / cm ³ .

(Negative electrode A7)
By mixing 8.5 g of the negative electrode active material SiO _x used in Example 1 and 1.5 g of the conductive auxiliary agent SuperP, and performing a mechanical surface fusion treatment by a mechanical alloy method, the surface is made conductive with SiO _x particles as a nucleus. Conductive SiO _x particles coated with a conductive material (SuperP). The content of the conductive substance in the conductive SiO _x particles was 15% by weight.

  A negative electrode A7 was produced in the same manner as in Example 1 except that the composition of the negative electrode slurry was as follows.

Negative electrode active material: 1.18 parts by weight of conductive SiO _x
8.45 parts by weight of carbon material Conductive aid: 0.20 parts by weight of SuperP Binder: 0.35 parts by weight of polyvinylidene fluoride (PVDF) Solvent: 10.0 parts by weight of N-methyl-2-pyrrolidone (NMP)

When this composition is applied to the formula (1), α (SiO _x ) + β (carbon material) = 96.3, α (SiO _x ) = 11.8, β (carbon material) = 84.5, and the formula (1 ) Satisfy the requirements. The weight of the negative electrode active material layer on one side of the negative electrode A7 was 8.54 mg / cm ² , and the density was 1.45 g / cm ³ .

(Negative electrode A8)
A negative electrode A8 was produced in the same manner as in Example 1 except that the composition of the negative electrode slurry was as follows.

Negative electrode active material: carbon material 9.45 parts by weight Conductive auxiliary agent: SuperP 0.20 parts by weight Binder: polyvinylidene fluoride (PVDF) 0.35 parts by weight Solvent: N-methyl-2-pyrrolidone (NMP) 10.0 parts by weight Department.

When this composition is applied to the formula (1), α (SiO _x ) = 0 and β (carbon material) = 94.5, which does not satisfy the requirement of the formula (1). The weight of the negative electrode active material layer on one side of the negative electrode A8 was 12.75 mg / cm ² , and the density was 1.45 g / cm ³ .

(Negative electrode A9)
A negative electrode A9 was produced according to Example 1 except that the composition of the negative electrode slurry was as follows.

Negative electrode active material: 9.45 parts by weight of SiO _x Conductive aid: 0.20 parts by weight of SuperP Binder: 0.35 parts by weight of polyvinylidene fluoride (PVDF) Solvent: N-methyl-2-pyrrolidone (NMP) 10.0 parts by weight Department.

When this composition is applied to the formula (1), α (SiO _x ) = 94.5 and β (carbon material) = 0, which does not satisfy the requirement of the formula (1). The weight of the negative electrode active material layer on one side of the negative electrode A9 was 2.55 mg / cm ² , and the density was 1.45 g / cm ³ .

In preparation of the negative electrodes A1 to A9, the charge capacity of the negative electrodes A2 to A9 is 4.70 mAh / cm in consideration of the irreversible capacity (particularly, the irreversible capacity of SiO _x ) in the negative electrode active material and the negative electrode slurry composition. ^The coating amount was adjusted to be ² . The composition of the obtained negative electrodes A1 to A9 and the measured values of the charge capacity and the discharge capacity are summarized in Table 2 below. In Table 2, “α” and “β” represent α (SiO _x ) and β (carbon material), respectively, and “γ” and “η” represent the binder and the conductive auxiliary in the negative electrode active material layer, respectively. Means weight percent.

  Next, the positive electrodes C1 to C13 obtained above and the negative electrodes A1 to A9 obtained above were combined as shown in Table 3 below to produce a battery according to Example 1 (Example 1). To 18 and Comparative Examples 1 to 5).

  Thereafter, the power generation element of each battery obtained above was set on an evaluation cell attachment jig, and a positive electrode lead and a negative electrode lead were attached to each tab end of the power generation element, and a test was performed.

[Evaluation of battery characteristics]
The laminate type battery produced above was subjected to initial charge treatment and activation treatment under the following conditions, and performance was evaluated.

[First charging process]
The battery aging treatment was performed as follows. At 25 ° C., the battery was charged at a constant current charging method of 0.05 C for 4 hours (SOC approximately 20%). Next, after charging to 4.45 V at a 0.1 C rate at 25 ° C., the charging was stopped and the state (SOC about 70%) was maintained for about 2 days (48 hours).

[Gas removal treatment 1]
One side temporarily sealed by thermocompression bonding was opened, gas was removed at 10 ± 3 hPa for 5 minutes, and then thermocompression bonding was performed again to perform temporary sealing. Further, pressurization with a roller (surface pressure 0.5 ± 0.1 MPa) was performed, and the electrode and the separator were sufficiently adhered.

[Activation processing]
After charging at 25 ° C. by a constant current charging method at 0.1 C until the voltage reached 4.45 V, a cycle of discharging to 0.1 V at 0.1 C was performed twice. Similarly, after charging at 25 ° C. to 4.55 V at 0.1 C by the constant current charging method, a cycle of discharging to 2.0 V at 0.1 C once is 4.65 V at 0.1 C. After being charged until it was, a cycle of discharging to 2.0 V at 0.1 C was performed once. Furthermore, the battery was charged at 25 ° C. by a constant current charging method until it reached 4.75 V at 0.1 C, and then discharged once to 2.0 V at 0.1 C.

[Gas removal process 2]
One side temporarily sealed by thermocompression bonding was opened, gas was removed at 10 ± 3 hPa for 5 minutes, and then thermocompression bonding was performed again to perform main sealing. Further, pressurization with a roller (surface pressure 0.5 ± 0.1 MPa) was performed, and the electrode and the separator were sufficiently adhered.

[Rate performance evaluation]
The rate performance of the battery is evaluated by a constant current / constant voltage charging method in which the battery is charged at a rate of 0.1 C until the maximum voltage reaches 4.5 V, and then held for about 1 hour to 1.5 hours. This was carried out by a constant current discharge method in which discharge was performed at a 0.1 C rate or a 2.5 C rate until the minimum voltage of 2.0 V became 2.0 V. All were performed at room temperature. The rate characteristics were evaluated as the ratio of the capacity at 2.5 C discharge to the capacity at 0.1 C discharge. The results are shown in Table 3 below.

[Life Evaluation]
In the battery life test, the above charge / discharge at the 1.0 C rate was repeated 100 cycles at 25 ° C. The battery is evaluated by a constant current / constant voltage charging method in which charging is performed at a rate of 0.1 C until the maximum voltage reaches 4.5 V, and then held for about 1 hour to 1.5 hours. The constant current discharge method was used in which discharge was performed at a 0.1 C rate until the minimum voltage reached 2.0V. All were performed at room temperature.

  The ratio of the discharge capacity at the 100th cycle to the discharge capacity at the first cycle was evaluated as “capacity maintenance ratio (%)”. The results are shown in Table 3 below.

  Capacity maintenance rate (%) = 100th cycle discharge capacity / first cycle discharge capacity × 100

  As is clear from the results shown in Table 3, in the lithium ion secondary batteries of Examples 1 to 18 which are electrical devices according to the present invention, the cycle characteristics (capacity maintenance at the 100th cycle) were compared with those of Comparative Examples 1 to 5. Rate) and rate characteristics (2.5C / 0.1C capacity retention ratio) showed excellent characteristics.

  In Comparative Example 1 and Comparative Example 4 using the negative electrode A8, sufficient rate characteristics cannot be achieved as the coating amount of the negative electrode active material layer becomes too large. On the other hand, in Comparative Example 2 and Comparative Example 5 using the negative electrode A9, the coating amount of the negative electrode active material layer was too small to achieve sufficient cycle durability. Further, when the positive electrode C13 containing a solid solution positive electrode active material in which Mn is not substituted with another metal is used, sufficient performance is achieved in both cycle durability and rate characteristics even when the negative electrode A1 is used. I couldn't.

10, 50 lithium ion secondary battery,
11 negative electrode current collector,
12 positive electrode current collector,
13 negative electrode active material layer,
15 positive electrode active material layer,
17 separator,
19 cell layer,
21, 57 power generation element,
25 negative current collector,
27 positive current collector,
29, 52 Battery exterior material,
58 positive electrode tab,
59 Negative electrode tab.

Claims (8)

A positive electrode in which a positive electrode active material layer containing a positive electrode active material is formed on the surface of the positive electrode current collector;
A negative electrode in which a negative electrode active material layer containing a negative electrode active material is formed on the surface of the negative electrode current collector;
A separator;
An electrical device having a power generation element comprising:
The coating amount of the negative electrode active material layer is 3 to 11 mg / cm ² ,
The negative electrode active material layer has the following formula (1):
In the formula, SiO _x is a mixture of amorphous SiO ₂ particles and Si particles, x represents the number of oxygen satisfying the valence of Si, and α (SiO _x ) and β (carbon material) are negative electrode active material layers Represents the% by weight of the SiO _x and carbon material in which, respectively, 80 ≦ α (SiO _x ) + β (carbon material) ≦ 98, 3 ≦ α (SiO _x ) ≦ 40, 40 ≦ β (carbon material) ≦ 95 ,
Contains a negative electrode active material is Ru represented in,
The positive electrode active material layer has the following formula (2):
In the formula, f (solid solution positive electrode active material) represents the weight% of the solid solution positive electrode active material in the positive electrode active material layer, and 80 ≦ f (solid solution positive electrode active material) ≦ 98.
Containing a positive electrode active material you express in this case, the solid solution positive electrode active material represented by the following formula (3):
In the formula, X is at least one selected from the group consisting of Ti, Zr and Nb, and 0.01 ≦ e ≦ 0.4, a + b + c + d + e = 1.5, 0.1 ≦ d ≦ 0.4, 1.1 ≦ [a + b + c + e] ≦ 1.4, and z represents the number of oxygen satisfying the valence.
An electrical device having a composition represented by:   The solid solution positive electrode active material has 20-23 °, 35-40 ° (101), 42-45 ° (104), and 64-65 (108) / 65-66 (110) in X-ray diffraction (XRD) measurement. The electric device according to claim 1, which has a diffraction peak indicating a rock salt type layered structure.   The electric device according to claim 1, wherein the solid solution positive electrode active material has substantially no peak attributed to other than a diffraction peak of a rock salt type layered structure in X-ray diffraction (XRD) measurement.   The solid solution positive electrode active material has three diffraction peaks at 35-40 ° (101) and one diffraction peak at 42-45 ° (104) in X-ray diffraction (XRD) measurement. The electrical device of any one of -3.   The solid solution positive electrode active material was measured at 20-23 °, 35.5-36.5 ° (101), 43.5-44.5 ° (104) and 64-65 (108) in X-ray diffraction (XRD) measurement. ) / 65-66 (110) has a diffraction peak, The electrical device of any one of Claims 1-4. The SiO _x is a mechanical surface fusion treatment SiO _x conductive SiO _x particles whose surface is coated with a conductive material particles by the content of the conductive material in the conductive SiO _x particles 1 The electrical device according to claim 1, wherein the electrical device is 30% by weight. The electrical device according to any one of claims 1 to 6, wherein an average particle diameter of the SiO _x is smaller than an average particle diameter of the carbon material.   The electrical device according to claim 1, which is a lithium ion secondary battery.