Patent Application
20160285073
This application claims priority from Japanese Patent Application No. 2015-066290 filed with the Japan Patent Office on Mar. 27, 2015, the entire content of which is hereby incorporated by reference.
1. Technical Field
The present disclosure relates to a positive electrode active material, a positive electrode using the same, and a lithium ion secondary battery.
2. Description of the Related Art
Conventionally, researches have been widely conducted on the use of lithium cobalt oxide, lithium nickel oxide, lithium manganese oxide and the like as the positive electrode active material for lithium ion secondary batteries, as these materials enable the generation of an electromotive force in excess of 4 V.
With regard to the positive electrode active material for lithium ion secondary batteries, there is a trend for increasing the charge voltage so as to achieve an increase in discharge capacity. However, when the discharge capacity is increased by increasing the charge voltage, the amount of heat generated by the battery also increases. The heat may degrade the cycle characteristics of the battery.
Particularly, in a battery system including lithium cobalt oxide, lithium nickel oxide, lithium manganese oxide, or the like as the positive electrode active material, sufficient cycle characteristics may not be obtained when there is a large amount of heat due to the increase in charge voltage. This problem is particularly pronounced in a high temperature environment.
The cycle characteristics of lithium cobalt oxide are disclosed in JP-A-2006-164758, for example. This literature reports that an improvement in cycle characteristics can be achieved by substituting part of cobalt and/or lithium of lithium cobalt oxide with another metal element. However, the improvement is still insufficient, and a further improvement in cycle characteristics is desired. In the following, the lithium ion secondary battery may be simply referred to as “the battery” depending on the context.
A positive electrode active material includes: a lithium complex oxide expressed by chemical formula (1); and a highly thermal conductive compound having thermal conductivity of 10 W/m·K or more, the chemical formula (1) being
LixM1yM21-yO2 (1)
where M1 is at least one metal selected from the group consisting of Ni, Co, and Mn, M2 is at least one metal selected from the group consisting of A, Fe, Ti, Cr, Mg, Cu, Ga, Zn, Sn, B, V, Ca, and Sr, and x and y are numbers such that 0.05≦x≦1.2 and 0.3≦y≦1.
In the following detailed description, for purpose of explanation, numerous specific details are set forth in order to provide a thorough understanding of the disclosed embodiments. It will be apparent, however, that one or more embodiments may be practiced without these specific details. In other instances, well-known structures and devices are schematically shown in order to simplify the drawing.
An object of the present disclosure is to provide a positive electrode active material, a positive electrode, and a lithium ion secondary battery with high cycle characteristics.
A positive electrode active material according to one aspect of the present disclosure (the present positive electrode active material) includes: a lithium complex oxide expressed by chemical formula (1); and a highly thermal conductive compound having thermal conductivity of 10 W/m·K or more, the chemical formula (1) being
LixM1yM21-yO2 (1)
where M1 is at least one metal selected from the group consisting of Ni, Co, and Mn, M2 is at least one metal selected from the group consisting of Al, Fe, Ti, Cr, Mg, Cn, Ga, Zn, Sn, B, V, Ca, and Sr, and x and y are numbers such that 0.05≦x≦1.2 and 0.3≦y≦1.
The present positive electrode active material with the configuration includes the highly thermal conductive compound with thermal conductivity of 10 W/m·K or more. Accordingly, the heat generated during charging is allowed to escape efficiently. As a result, the accumulation of heat in the positive electrode can be suppressed, whereby deterioration of the present positive electrode active material can be suppressed. In this way, cycle characteristics are improved. When the charge voltage is raised to around 4.2 V, in particular, crystal transition of the positive electrode active material, or decomposition of the positive electrode active material may occur, possibly resulting in large heat generation. Such decrease in the thermal stability of the positive electrode active material can be suppressed by the present positive electrode active material having the above configuration.
In the present positive electrode active material, the highly thermal conductive compound may be at least one selected from the group consisting of AlN, BN, Si3N4, TiN, ZrN, VN, Cr2N, SiC, WC, TiC, TaC, ZrC, NbC, Mo2C, Cr3C2, TiB2, ZrB2, VB2, and NbB2.
According to this configuration, the present positive electrode active material includes compounds with particularly high thermal conductivity. In this way, the heat generated during charging is allowed to escape efficiently. As a result, the accumulation of heat in the positive electrode can be suppressed, whereby deterioration of the present positive electrode active material can be suppressed. Accordingly, cycle characteristics are improved.
In the present positive electrode active material, the highly thermal conductive compound may be at least one selected from the group consisting of AlN, BN, Si3N4, TiN, ZrN, VN, NbN, and Cr2N.
Nitride is very stable. Accordingly, a lithium complex oxide and nitride do not readily react with each other. Thus, cycle characteristics are improved.
The lithium complex oxide used for the present positive electrode active material may be expressed by chemical formula (2):
LiaNi1-bM3bO2 (2)
where M3 is at least one metal selected from the group consisting of Co, Fe, Ti, Cr, Mg, Al, Cu, Ga, Mn, Za, Sn, B, V, Ca, and Sr, and a and b are numbers such that 0.05≦a≦1.2 and 0≦b≦0.5.
In this case, the present positive electrode active material includes a lithium complex oxide with a high Ni ratio. In this way, the discharge capacity is increased.
The highly thermal conductive compound (weight) used for the present positive electrode active material may have a content of 0.05 to 10 wt % with respect to the lithium complex oxide.
When the weight of the highly thermal conductive compound relative to the lithium complex oxide is more than 0.05 wt %, the heat generated during charging can escape more efficiently. As a result, cycle characteristics are improved. When the weight of the highly thermal conductive compound relative to the lithium complex oxide is not more than 10 wt %, a decrease in energy density can be suppressed.
The highly thermal conductive compound used for the present positive electrode active material may coat at least a part of the lithium complex oxide.
When at least a part of the lithium complex oxide is coated by the highly thermal conductive compound, the heat from a heat-generating source can be transmitted and allowed to escape more efficiently. As a result, the accumulation of heat in the positive electrode is suppressed, whereby deterioration of the present positive electrode active material is suppressed. Thus, cycle characteristics are improved.
The highly thermal conductive compound used for the present positive electrode active material may have an average primary particle diameter of 10 to 500 nm.
When the average primary particle diameter of the highly thermal conductive compound is 10 nm or more, a thermal conduction network path can be more readily formed, enabling the heat to escape efficiently. When the average primary particle diameter of the highly thermal conductive compound is 500 nm or less, the number of points of contact between the particles can be increased, enabling the heat to escape efficiently. As a result, cycle characteristics are improved.
According to embodiments of the present disclosure, there are provided a positive electrode active material, a positive electrode using the same, and a lithium ion secondary battery which have high cycle characteristics.
An example of a preferred embodiment of the lithium ion secondary battery according to the present disclosure will be described with reference to the drawings. It should be noted, however, that the lithium ion secondary battery according to the present disclosure is not limited to the following embodiments. The dimensional ratios of the drawings are not limited to the illustrated ratios.
The electrodes and the lithium ion secondary buttery according to the present embodiment will be briefly described with reference to
In the stacked body 40, a positive electrode 20 and a negative electrode 30 are disposed opposite each other across a containing a nonaqueous electrolyte. The positive electrode 20 includes a plate-like (film) positive electrode current collector 22, and a positive electrode active material layer 24 disposed on the positive electrode current collector 22. The negative electrode 30 includes a plate-like (film) negative electrode current collector 32 and a negative electrode active material layer 34 disposed on the negative electrode current collector 32. The positive electrode active material layer 24 and the negative electrode active material layer 34 are in contact with corresponding sides of the separator 10. To corresponding edge parts of the positive electrode current collector 22 and the negative electrode current collector 32, leads 62, 60 are connected. Edge parts of the leads 60, 62 are disposed outside the case 50.
In the following, the positive electrode 20 and the negative electrode 30 may be collectively referred to as the electrode 20, 30. The positive electrode current collector 22 and the negative electrode current collector 32 may be collectively referred to as the current collector 22, 32. The positive electrode active material layer 24 and the negative electrode active material layer 34 may be collectively referred to as the active material layer 24, 34.
The positive electrode active material layer according to the present embodiment includes a positive electrode active material, a positive electrode binder, and a conductive material.
A positive electrode active material according to the present embodiment includes: a lithium complex oxide expressed by chemical formula (1); and a highly thermal conductive compound having thermal conductivity of 10 W/m·K or more, the chemical formula (1) being
LixM1yM21-yO2 (1)
where M1 is at least one metal selected from the group consisting of Ni, Co, and Mn, M2 is at least one metal selected from the group consisting of Al, Fe, Ti, Cr, Mg, Cu, Ga, Zn, Sn, B, V, Ca, and Sr, and x and y are numbers such that 0.05≦x≦1.2 and 0.3≦y≦1.
According to this configuration, this positive electrode active material includes a highly thermal conductive compound having thermal conductivity of 10 W/m·K or mom. In this way, the heat generated during charging is allowed to escape efficiently. As a result, the accumulation of heat in the positive electrode can be suppressed, whereby deterioration of this positive electrode active material can be suppressed. Accordingly, cycle characteristics are improved.
The highly thermal conductive compound may have thermal conductivity higher than that of at least the lithium complex oxide included in the positive electrode active material. In this electrode active material, the highly thermal conductive compound is at least one selected from the group consisting of AlN, BN, Si3N4, TiN, ZrN. VN, TaN, Cr2N, SiC, WC, TiC, TaC, ZaC, NbC, Mo2C, Cr3C2, TiB2, ZrB2, VB2, and NbB2. According to this configuration, the present positive electrode active material includes compounds with particularly high thermal conductivity. In this way, the heat generated during charging is allowed to escape efficiently. As a result, the accumulation of heat in the positive electrode can be suppressed, whereby deterioration of the present positive electrode active material can be suppressed. Accordingly, cycle characteristics are improved.
In this positive electrode active material, the highly thermal conductive compound may be at least one selected from the group consisting of AlN, BN, Si3N4, TiN, ZrN, VN, NbN, and Cr2N. Nitride is very stable. Accordingly, a lithium complex oxide and nitride do not readily react with each other. Thus, cycle characteristics are improved.
The lithium complex oxide used for this positive electrode active material may be expressed by chemical formula (2):
LiaNi1-bM3bO2 (2)
where M3 is at least one metal selected from the group consisting of Co, Fe, Ti, Cr, Mg, Al, Cu, Ga, Mn, Zn, Sn, B, V, Ca, and Sr, and a and b are numbers such that 0.05≦a≦1.2 and 0≦b≦0.5.
In this case, the present positive electrode active material includes a lithium complex oxide with a high Ni ratio. In this way, the discharge capacity is increased.
The highly thermal conductive compound (weight) used for this positive electrode active material may have a content of 0.05 to 10 wt % with respect to the lithium complex oxide. When the weight of the highly thermal conductive compound relative to the lithium complex oxide is more than 0.05 wt %, the heat generated during charging can escape more efficiently. As a result, cycle characteristics are improved. When the weight of the highly thermal conductive compound relative to the lithium complex oxide is not more than 10 wt %, a decrease in energy density can be suppressed.
The weight of the highly thermal conductive compound relative to the lithium complex oxide may be 0.1 to 5 wt % When the weight of the highly thermal conductive compound relative to lithium complex oxide is 0.1 to 5 wt %, the above described effect can be enhanced.
As described above, the positive electrode active material according to the present embodiment contains a specific lithium complex oxide and a highly thermal conductive compound with thermal conductivity of 10 W/m·K or more. The form of the active material is not particularly limited as long as the highly thermal conductive compound is in contact with the particle surface of the lithium complex oxide. Namely, the lithium complex oxide and the highly thermal conductive compound only need to be mixed in the positive electrode active material layer 24. With regard to the mixed state, the highly thermal conductive compound may be uniformly dispersed in the positive electrode active material layer 24. Alternatively, the lithium complex oxide and the highly thermal conductive compound may be mutually aggregated, forming secondary particles.
In order to improve cycle characteristics, the highly thermal conductive compound may coat at least a part of the lithium complex oxide. In this way, heat from a heat generating source can be more efficiently transmitted and allowed to escape. As a result, deterioration of the positive electrode active material can be suppressed, whereby cycle characteristics are improved. An example of this form is illustrated in
The lithium complex oxide 110 may further constitute secondary particles. The secondary particle may be at least partially coated by the highly thermal conductive compound 120.
In the state illustrated in
Thus, the highly thermal conductive compound 120 (120G) may fill the gaps between the primary particles of the lithium complex oxide 110 that are present in the vicinity of the surface of the secondary particles of the lithium complex oxide 110. With regard to the average particle diameter of the primary particles of the highly thermal conductive compound 120, the average particle diameter of the highly thermal conductive compound 120G filling the gaps between the primary particles of the lithium complex oxide 110 may be smaller than that of the highly thermal conductive compound 120S present on the surface of the secondary particles of the lithium complex oxide 110. According to this configuration, composite particles with increased density can be obtained.
The highly thermal conductive compound used for the positive electrode active material may have an average primary particle diameter of 10 to 500 nm. When the average primary particle diameter of the highly thermal conductive compound is 10 nm or more, a thermal conduction network path can be more readily formed, enabling the heat to escape efficiently. When the average primary particle diameter of the highly thermal conductive compound is 500 nm or less, the number of points of contact between the particles can be increased, enabling the heat to escape efficiently. As a result, cycle characteristics are improved. The average primary particle diameter can be determined from the cross section of the positive electrode active material layer. For example, the primary particle diameters of 50 particles of the highly thermal conductive compound are sampled using a scanning electron microscope (SEM), and their average value is computed.
Examples of the lithium complex oxide according to the present embodiment include nickel-cobalt-aluminum (NCA) ternary materials such as Li1.0Ni0.83Co0.14Al0.03O2.0 and Li1.0Ni0.8Co0.15Al0.05O2.0; nickel-cobalt-manganese (NCM) ternary materials such as Li1.0Ni0.8Co0.1Mn0.1O2.0, Li1.0Ni0.5Co0.2Mn0.3O2.0, Li1.0Ni0.6Co0.2Mn0.2O2.0, and Li1.0Ni0.333Co0.333Mn0.333O2.0; and lithium cobalt oxide (LCO) such as LiCoO2. Among others, NCA may be preferable as it has high energy density.
The lithium complex oxide according to the present embodiment may be a mixture of two or more of the aforementioned lithium complex oxides.
The type of the lithium complex oxide and highly thermal conductive compound included in the positive electrode active material according to the present embodiment can be identified by X-ray diffraction, X-ray photoelectron spectrometry, or energy dispersive X-ray spectrometry analysis. Among others, X-ray diffraction may preferably be used. The mixing ratios of the components may be identified by inductively coupled plasma optical emission spectrometry, for example.
According to the present embodiment, the state of coating and the like of the particle surface of the lithium complex oxide by the highly thermal conductive compound may be observed or measured as follows. For example, the positive electrode is cut and the section is polished by a cross section polisher or an ion milling device. The polished section is observed or measured by using a scanning electron microscope, a transmission electron microscope, or the like.
The positive electrode current collector 22 may be a plate of conductive material. For example, as the positive electrode current collector 22, a metal thin plate with an aluminum, copper, or nickel foil may be used.
Examples of the conductive material include carbon powder of carbon black and the like; carbon nanotube; carbon material; metal fine powder of copper, nickel, stainless, or iron; mixtures of carbon material and metal fine powder; and conductive oxides such as ITO.
The binder binds the active materials and also binds the active materials with the current collector 22. The binder may be any binder capable of achieving the above binding. Examples of the binder include fluorine resin such as polyvinylidene fluoride (PVDF), polytetrafluoroethylene (PTFE), tetrafluoroethylene/hexafluoropropylene copolymer (FEP), tetrafluoroethylene/perfluoro alkyl vinyl ether copolymer (PFA), ethylene/tetrafluoromethylene copolymer (ETFE), polychlorotrifluoroethylene (PCTFE), ethylene/chlorotrifluoroethylene copolymer (ECTFE), and polyvinyl fluoride (PVF).
Other than the above examples, vinylidene fluoride fluorine rubber may be used as the binder. Examples of fluorine rubber based on vinylidene fluoride include fluorine rubber based on vinylidene fluoride/hexafluoropropylene (VDF/HFP-based fluorine rubber), fluorine rubber based on vinylidene fluoride/hexafluoropropylene/tetrafluoroethylene (VDF/HFPTFE-based fluorine rubber), fluorine rubber based on vinylidene fluoride/pentafluoropropylene (VDF/PFP-based fluorine rubber), fluorine rubber based on vinylidene fluoride/pentafluoropropylene/tetrafluoroethylene (VDF/PFP/TFE-based fluorine rubber), fluorine rubber based on vinylidene fluoride/perfluoromethyl vinyl ether/tetrafluoroethylene (VDF/PFMVE/TFE-based fluorine rubber), and fluorine rubber based on vinylidene fluoride/chlorotrifluoroethylene (VDF/CTFE-based fluorine rubber).
As the binder, a conductive polymer having electronic conductivity or conductive polymer having ion conductivity may be used. An example of the conductive polymer having electronic conductivity is polyacetylene. In this case, the binder will also serve as conductive material, so that other conductive material may not be added. An example of the conductive polymer having ion conductivity is a composite of polymer compound, such as polyethylene oxide or polypropylene oxide, and a lithium salt or an alkali metal salt based on lithium.
The negative electrode active material layer according to the present embodiment includes a negative electrode active material, a negative electrode binder, and a conductive material.
The negative electrode active material may be a compound capable of lithium ion intercalation and deintercalation. As the negative electrode active material, known negative electrode active material for lithium-ion batteries may be used. As the negative electrode active material, substance capable of lithium ion intercalation and deintercalation may be used. Examples of such substance include carbon material such as graphite (natural graphite and synthetic graphite), carbon nanotube, hard carbon, soft carbon, and low temperature heat-treated carbon; metals that can be combined with lithium, such as aluminum, silicon, and tin; amorphous compound based on an oxide such as silicon dioxide and tin dioxide; and particles including lithium titanate (Li4Ti5O12) or the like. The negative electrode active material may be graphite, which has high capacity per unit weight and is relatively stable.
The negative electrode current collector 32 may be a plate of conductive material. As the negative electrode current collector 32, a metal thin plate including aluminum, copper, or nickel foil may be used.
Examples of the conductive material include carbon material such as carbon powder of carbon black and the like, and carbon nanotube; metal fine powder of copper, nickel, stainless, or iron; a mixture of carbon material and metal fine powder and conductive oxide such as ITO.
As the binder used in the negative electrode, materials similar to those for the positive electrode may be used.
The material of the separator 10 may have an electrically insulating porous structure. Examples of the material include a single-layer body or stacked body of polyethylene, polypropylene, or polyolefin film; extended film of a mixture of the aforementioned resins; and fibrous nonwoven fabric including at least one constituent material selected from the group consisting of cellulose, polyester, and polypropylene.
The non-aqueous electrolyte includes electrolyte dissolved in non-aqueous solvent. The non-aqueous solvent may contain cyclic carbonate and chain carbonate.
The cyclic carbonate is not particularly limited as long as it is capable of solvating the electrolyte, and known cyclic carbonate may be used. Examples of the cyclic carbonate include ethylene carbonate, propylene carbonate, and butylene carbonate.
The chain carbonate is not particularly limited as long as it is capable of decreasing the viscosity of the cyclic carbonate, and known chain carbonate may be used. Examples of the chain carbonate include diethyl carbonate, dimethyl carbonate, and ethyl methyl carbonate. As the chain carbonate, there may be used a mixture of methyl acetate, ethyl acetate, methyl propionate, ethyl propionate, γ-butyrolactone, 1,2-dimethoxyethane, 1,2-diethoxyethane, and the like.
The ratio of the cyclic carbonate and the chain carbonate in the non-aqueous solvent may be 1:9 to 1:1 by volume.
Examples of the electrolyte include lithium salts such as LiPF6, LiCO4, LiBF4, LiCF3SO3, LiCF3, CF2SO3, LiC(CF3SO2)3, LiN(CF3SO2)3, LiN(CF3CF2SO2)2, LiN(CF3SO2)(C4F9SO2), LiN(CF3CF2CO)2, and LiBOB. Any of the lithium salts may be used individually, or two or more lithium salts may be used in combination. Particularly, from the viewpoint of electrical conductivity, the electrolyte may preferably include LiPF6.
When LiPF6 is dissolved in non-aqueous solvent, the concentration of the electrolyte in the non-aqueous electrolyte may be adjusted to 0.5 to 2.0 mol/L. When the electrolyte concentration is 0.5 mol/L or more, sufficient conductivity of the non-aqueous electrolyte can be ensured. As a result, sufficient capacity can be more readily obtained during charging/discharging. Further, by limiting the electrolyte concentration to 2.0 mol/1 or less, an increase in the viscosity of the non-aqueous electrolyte can be suppressed, and sufficient lithium ion mobility can be ensured. As a result, sufficient capacity can be more readily obtained during charging/discharging.
When LiPF6 is mixed with other electrolytes, the lithium ion concentration in the non-aqueous electrolyte may be adjusted to 0.5 to 2.0 mol/L. Of the lithium ions in the non-aqueous electrolyte, the lithium ions from LiPF6 may have a concentration of 50 mol % or more.
The positive electrode active material according to the present embodiment may be manufactured through the following mixing step and coating step.
In the mixing step, the lithium complex oxide and the highly thermal conductive compound are mixed to obtain the positive electrode active material. The mixing method Is not particularly limited. For example, mixing is performed using an existing device, such as a Turbula mixer or a Henschel mixer.
In the coating step, the high thermal conductive compound is coated on a surface of the lithium complex oxide 110, whereby the coating layer 120 is formed. The method for forming the coating layer 120 is not particularly limited, and a conventional method may be used to form the coating layer 120 on the particle surface. Examples of the method include mechanochemical methods using mechanical energy, such as friction and compression, and a spray dry method of spraying coating liquid onto the particles. Among others, the mechanochemical method may be preferable as it enables formation of uniform coating layers 120 with good adhesion.
A method for manufacturing the electrode 20 and 30 according to the present embodiment will be described.
The active material, binder, and solvent are mixed to prepare a paint. If necessary, conductive material may be further added. As the solvent, water or N-methyl-2-pyrrolidone may be used. The method of mixing the components of the paint is not particularly limited. The order of mixing is also not particularly limited. The paint is coated onto the current collectors 22 and 32. The coating method is not particularly limited, and a method typically adopted for electrode fabrication may be used. The coating method may include slit die coating and doctor blade method.
Thereafter, the solvent in the paint coating the current collectors 22 and 32 is removed. The removing method is not particularly limited, and may include drying the current collectors 22 and 32 with the paint coat thereon in an atmosphere of 80° C. to 150° C.
The resulting electrodes with the positive electrode active material layer 24 and the negative electrode active material layer 34 respectively formed thereon are pressed by a roll press device or the like as needed. The roll press may have a linear load of 100 to 2500 kgf/cm, for example.
Through the above-described steps, there are obtained the positive electrode 20 including the positive electrode current collector 22 with the positive electrode active material layer 24 formed thereon, and the negative electrode 30 including the negative electrode current collector 32 with the negative electrode active material layer 34 formed thereon.
In the following, a method for manufacturing the lithium ion secondary battery 100 according to the present embodiment will be described. The method for manufacturing the lithium ion secondary battery 100 according to the present embodiment includes a step of sealing, in the case (exterior body) 50, the positive electrode 20 and the negative electrode 30 including the above-described active materials, the separator 10 to be disposed between the positive electrode 20 and the negative electrode 30, and the nonaqueous electrolytic solution including lithium salt.
For example, the positive electrode 20 and the negative electrode 30 including the above-described active materials, and the separator 10 are stacked. The positive electrode 20 and the negative electrode 30 are heated and pressed from a direction perpendicular to the stacked direction, using a pressing tool. In this way, the stacked body 40 including the positive electrode 20, the separator 10, and the negative electrode 30 that are mutually closely attached is obtained. The stacked body 40 is then put into a pre-fabricated bag of the case 50, for example, and additionally the nonaqueous electrolytic solution including the above-described lithium salt is injected. In this way, the lithium ion secondary battery 100 is fabricated. Instead of injecting the nonaqueous electrolytic solution including the lithium salt into the case 50, the stacked body 40 may be impregnated in advance in a nonaqueous electrolytic solution including the lithium salt.
It should be noted, however, that the present disclosure is not limited to the embodiment, and that the embodiment is merely illustrative. Any and all configurations that are substantially identical, either in operation or effect, to the technical concept set forth in the claims are included in the technical scope of the present disclosure.
Lithium complex oxide of Li1.0Ni0.83Co0.14Al0.03O2.0 (hereafter referred to as NCA) and AlN (from IoLiTec GmbH) with an average particle diameter of 50 an were weighted at a mass ratio of 100:0.1. The surface of NCA was coated by AlN by a mechanochemical method, obtaining positive electrode active material. The active material was mixed with a binder of polyvinylidene fluoride (PVDF) and acetylene black, and the mixture was dispersed in a solvent of N-methyl-2-pyrrolidone (NMP), preparing a slurry. The slurry was prepared such that the weight ratio of the positive electrode active material, acetylene black, and PVDF in the slurry was 93:3:4. The slurry was applied to an aluminum foil with a thickness of 20 μm for the current collector, dried, and then rolled at a linear load of 1000 kgf/cm. In this way, the positive electrode of Example 1 was obtained.
The state of coating of the lithium complex oxide particle surface by AlN was observed (measured) by using a transmission electron microscope (TEM), a scanning electron microscope (SEM), energy dispersive X-ray (EDX) spectrometry analysis, a cross section polisher, and an ion milling device. Samples to be subjected to measurement were fabricated by cutting the positive electrode and polishing the cross section using the cross section polisher and the ion milling device.
By the observation of the positive electrode surface and the positive electrode cross section by the SEM, EDX, and the TEM, formation of a uniform AlN coating on the lithium complex oxide particle surface was confirmed.
A slurry was prepared by dispersing 90 parts by mass of natural graphite powder as the negative electrode active material and 10 parts by mass of PVDF in NMP. The slurry was applied to a copper foil with a thickness of 15 μm. The copper foil with the slurry applied thereon was dried under reduced pressure at a temperature of 140° C. for 30 minutes, and then pressed using a roll press device. In this way, the negative electrode was obtained.
In a mixture solvent of ethylene carbonate (EC) and diethyl carbonate (DEC), LiPF6 was dissolved to 1.0 mol/L, whereby a nonaqueous electrolyte was obtained. In the mixture solvent, the volume ratio of EC and DEC was EC:DEC=30:70.
A polyethylene porous film (pore ratio: 40%, shutdown temperate 134° C.) with a film thickness of 16 μm was prepared.
A generator element was constructed by stacking the positive electrode, the negative electrode, and the separator. The generator element and the non-aqueous electrolyte were used to fabricate a battery cell according to Example 1.
The current density such that the battery cell capacity is constant-current discharged in an hour in an environment of 25° C. is referred to as 1 C. In the following, the current density at the time of charging or discharging will be expressed using constant multiples of the C rate (for example, the current density of one tenth of 1 C will be expressed as 0.1 C).
Using the battery cell of Example 1, constant-current charging was performed at the current density of 0.1 C until voltage reached 4.2 V (vs. Li/Li+). Further, constant-voltage charging was performed at 4.2 V (vs. Li/Li+) until the current density decreased to 0.05 C, when the charge capacity was measured. The results are shown in Table 1 in terms of 0.1 C discharge capacity.
After a pause of 5 minutes, constant-current discharging was performed at the current density of 0.1 C until voltage reached 2.5 V (vs. Li/Li+), when the discharge capacity was measured. The current density was calculated assuming that 1 C corresponded to 186 mAh/g with respect to the amount of the positive electrode active material. Greater discharge capacity is more preferable.
The battery cell after the rate measurement was subjected to 100 cycles of the charging/discharging procedure at 0.5 C charge/1 C discharge. The charging and discharging were performed in a constant temperature bath at 45° C. With respect to the initial discharge capacity of 100%, the value of discharge capacity after 100 cycles was taken as the capacity retention. Further, five battery cells fabricated under the identical conditions were prepared, and an average value of their capacity retention was calculated. Greater capacity retention is more preferable. The calculated results are shown in Table 1 as the average values of capacity retention after 100 cycles.
The battery of Example 2 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, the mass ratio of lithium complex oxide and AlN was 100:0.03.
The battery of Example 3 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, the mass ratio of lithium complex oxide and AlN was 100:0.05.
The battery of Example 4 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, the mass ratio of lithium complex oxide and AlN was 100:1.
The battery of Example 5 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, the mass ratio of lithium complex oxide and AlN was 100:5.
The battery of Example 6 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, the mass ratio of lithium complex oxide and AlN was 100:10.
The battery of Example 7 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, the mass ratio of lithium complex oxide and AlN was 100:11.
The battery of Example 8 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, BN was used instead of AlN.
The battery of Example 9 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, BN was used instead of AlN, and that the weight ratio of lithium complex oxide and BN was 100:5.
The battery of Example 10 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode. Si3N4 was used instead of AlN.
The battery of Example 11 was fabricated and evaluated in the same way as in Example 1 with the exception (that, during the fabrication of the positive electrode, Si3N4 was used instead of AlN, and that the weight ratio of lithium complex oxide and Si3N4 was 100:5.
The battery of Example 12 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, TiN was used instead of AlN.
The battery of Example 13 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, ZrN was used instead of AlN.
The battery of Example 14 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, VN was used instead of AlN.
The battery of Example 15 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, Cr2N was used instead of AlN.
The battery of Example 16 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, SiC was used instead of AlN.
The battery of Example 17 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, WC was used instead of AlN.
The battery of Example 18 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode. TiC was used instead of AlN.
The battery of Example 19 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, TaC was used instead of AlN.
The battery of Example 20 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, ZrC was used instead of AlN.
The battery of Example 21 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, NbC was used instead of AlN.
The battery of Example 22 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, Cr3C2 was used instead of AlN.
The battery of Example 23 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, Mo2C was used instead of AlN.
The battery of Example 24 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, TiB2 was used instead of AlN.
The battery of Example 25 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, ZrB2 was used Instead of AlN.
The battery of Example 26 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, VB2 was used instead of AlN.
The battery of Example 27 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, NbB2 was used instead of AlN.
The battery of Example 28 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, lithium complex oxide and AlN were mixed by using a Turbula mixer without performing the step of coating the lithium complex oxide with AlN. In the positive electrode active material fabricated using the Turbula mixer, the lithium complex oxide and the highly thermal conductive compound of AlN were uniformly mixed.
The battery of Example 29 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, BN was used instead of AlN, and that the lithium complex oxide and BN were mixed using the Turbula mixer without performing the step of coating the lithium complex oxide.
The battery of Example 30 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, Si3N4 was used instead of AlN, and that lithium complex oxide and Si3N4 were mixed using the Turbula mixer without performing the step of coating the lithium complex oxide.
The battery of Example 31 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, AlN with an average primary particle diameter of 10 nm was used instead of AlN with the average primary particle diameter of 50 nm.
The battery of Example 32 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode. AlN with an average primary particle diameter of 100 nm was used instead of AlN with the average primary particle diameter 50 nm.
The battery of Example 33 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, AlN with an average primary particle diameter 500 nm was used instead of AlN with an average primary particle diameter 50 nm.
The battery of Example 34 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, lithium complex oxide of Li1.0Ni0.8Co0.1Al0.1O2.0 was used instead of the lithium complex oxide of Li1.0Ni0.83Co0.14Al0.03O2.0.
The battery of Example 35 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, lithium complex oxide of Li1.0Ni0.8Co0.1Mn0.1O2.0 was used instead of the lithium complex oxide of Li1.0Ni0.83Co0.14Al0.03O2.0, and that, during the discharge capacity measurement, the current density of 1 C was computed as 160 mAh/g with respect to the amount of the positive electrode active material.
The battery of Example 36 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, lithium complex oxide of Li1.0Ni0.5Co0.2Mn0.3O2.0 was used instead of the lithium complex oxide of Li1.0Ni0.83Co0.14Al0.03O2.0, and that, during the discharge capacity measurement, the current density of 1 C was computed as 160 mAh/g with respect to the amount of the positive electrode active material.
The battery of Example 37 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, lithium complex oxide of Li1.0Ni0.34Co0.33Mn0.33O2.0 was used instead of the lithium complex oxide of Li1.0Ni0.83Co0.14Al0.03O2.0, and that, during the discharge capacity measurement, the current density of 1 C was computed as 160 mAh/g with respect to the amount of the positive electrode active material.
The battery of Example 38 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, lithium complex oxide of Li1.0Ni0.6Co0.2Mn0.2O2.0 was used instead of the lithium complex oxide of Li1.0Ni0.83Co0.14Al0.03O2.0, and that, during the discharge capacity measurement, the current density of 1 C was computed as 160 mAh/g with respect to the amount of the positive electrode active material.
The battery of Example 39 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, lithium complex oxide of LiCoO2 was used instead of the lithium complex oxide of Li1.0Ni0.83Co0.14Al0.53O2.0, and that, during the discharge capacity measurement, the current density of 1 C was computed as 160 mAh/g with respect to the amount of the positive electrode active material.
The battery of Example 40 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, lithium complex oxide of Li1.0Ni0.9Co0.07Al0.03O2.0 in the form of spherical secondary particles was used instead of the lithium complex oxide of Li1.0Ni0.83Co0.14Al0.03O2.0. When the cross section of the positive electrode was observed by the TEM, the presence of the structure illustrated in
The battery of Example 41 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, instead of the lithium complex oxide of Li1.0Ni0.83Co0.14Al0.03O2.0, lithium complex oxide of Li1.0Ni0.7Co0.27Al0.03O2.0 in the form of spherical secondary particles was used. When the cross section of the positive electrode was observed by the TEM, the structure illustrated in
The battery of Comparative Example 1 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, AlN was not used.
The battery of Comparative Example 2 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, AlN was not used, and that, instead of the lithium complex oxide of Li1.0Ni0.83Co0.14Al0.03O2.0, lithium complex oxide of Li1.0Ni0.8Co0.1Al0.1O2.0 was used.
The battery of Comparative Example 3 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, AlN was not used; that, instead of the lithium complex oxide of Li1.0Ni0.83Co0.14Al0.03O2.0, lithium complex oxide of Li1.0Ni0.8Co0.1Mn0.1O2.0 was used; and that, during the discharge capacity measurement, the current density of 1 C was computed as 160 mAh/g with respect to the amount of the positive electrode active material.
The battery of Comparative Example 4 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, AlN was not used; that, instead of the lithium complex oxide of Li1.0Ni0.83Co0.14Al0.03O2.0, lithium complex oxide of Li1.0Ni0.5Co0.2Mn0.3O2.0 was used; and that, during the discharge capacity measurement, the current density of 1 C was computed as 160 mAh/g with respect to the amount of the positive electrode active material.
The battery of Comparative Example 5 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, AlN was not used; that, instead of the lithium complex oxide of Li1.0Ni0.83Co0.14Al0.03O2.0, lithium complex oxide of Li1.0Ni0.34Co0.33Mn0.33O2.0 was used; and that, during the discharge capacity measurement, the current density of 1 C was computed as 160 mAh/g with respect to the amount of the positive electrode active material.
The battery of Comparative Example 6 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive elected, AlN was not used; that, instead of the lithium complex oxide of Li1.0Ni0.83Co0.14Al0.03O2.0, lithium complex oxide of Li1.0Ni0.6C0.2Mn0.2O2.0 was used; and that, during the discharge capacity measurement, the current density of 1 C was computed as 160 mAh/g with respect to the amount of the positive electrode active material.
The battery of Comparative Example 7 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, AlN was not used; that, instead of the lithium complex oxide of Li1.0Ni0.83Co0.14Al0.03O2.0, lithium complex oxide of LiCoO2 was used; and that, during the discharge capacity measurement, the current density of 1 C was computed as 160 mAh/g with respect to the amount of the positive electrode active material.
The battery of Comparative Example 8 was fabricated and evaluated in the same way as in Example 1 with the exception that, during the fabrication of the positive electrode, SiO2 was used instead of AlN.
As will be seen from the results in Table 1, in the batteries according to Examples, lithium complex oxides and highly thermal conductive compounds are included in the positive electrode active material. Consequently, the capacity retention after 100 cycles is increased, and the cycle characteristics are improved.
The foregoing detailed description has been presented for the purposes of illustration and description. Many modifications and variations are possible in light of the above teaching. It is not intended to be exhaustive or to limit the subject matter described herein to the precise form disclosed. Although the subject matter has been described in language specific to structural features and/or methodological acts, it is to be understood that the subject matter defined in the appended claims is not necessarily limited to the specific features or acts described above. Rather, the specific features and acts described above are disclosed as example forms of implementing the claims appended hereto.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2015-066290 | Mar 2015 | JP | national |
| 2015-226174 | Nov 2015 | JP | national |
