WO2014080903A1 - Électrode négative pour dispositif électrique et dispositif électrique l'utilisant - Google Patents

Électrode négative pour dispositif électrique et dispositif électrique l'utilisant Download PDF

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WO2014080903A1
WO2014080903A1 PCT/JP2013/081158 JP2013081158W WO2014080903A1 WO 2014080903 A1 WO2014080903 A1 WO 2014080903A1 JP 2013081158 W JP2013081158 W JP 2013081158W WO 2014080903 A1 WO2014080903 A1 WO 2014080903A1
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negative electrode
alloy
active material
capacity
electrode active
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PCT/JP2013/081158
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English (en)
Japanese (ja)
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貴志 真田
渡邉　学
文博 三木
健介 山本
千葉　啓貴
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日産自動車株式会社
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    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/13—Electrodes for accumulators with non-aqueous electrolyte, e.g. for lithium-accumulators; Processes of manufacture thereof
    • H01M4/133—Electrodes based on carbonaceous material, e.g. graphite-intercalation compounds or CFx
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/13—Electrodes for accumulators with non-aqueous electrolyte, e.g. for lithium-accumulators; Processes of manufacture thereof
    • H01M4/134—Electrodes based on metals, Si or alloys
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/36—Selection of substances as active materials, active masses, active liquids
    • H01M4/38—Selection of substances as active materials, active masses, active liquids of elements or alloys
    • H01M4/386—Silicon or alloys based on silicon
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/36—Selection of substances as active materials, active masses, active liquids
    • H01M4/38—Selection of substances as active materials, active masses, active liquids of elements or alloys
    • H01M4/46—Alloys based on magnesium or aluminium
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/36—Selection of substances as active materials, active masses, active liquids
    • H01M4/58—Selection of substances as active materials, active masses, active liquids of inorganic compounds other than oxides or hydroxides, e.g. sulfides, selenides, tellurides, halogenides or LiCoFy; of polyanionic structures, e.g. phosphates, silicates or borates
    • H01M4/583—Carbonaceous material, e.g. graphite-intercalation compounds or CFx
    • H01M4/587—Carbonaceous material, e.g. graphite-intercalation compounds or CFx for inserting or intercalating light metals
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
    • Y02E60/10—Energy storage using batteries

Definitions

  • the present invention relates to a negative electrode for an electric device and an electric device using the same.
  • the negative electrode for an electric device and the electric device using the same according to the present invention are used as, for example, a driving power source or an auxiliary power source for a motor of a vehicle such as an electric vehicle, a fuel cell vehicle, and a hybrid electric vehicle as a secondary battery or a capacitor. It is done.
  • lithium ion secondary batteries 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 for 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.
  • 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.
  • 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
  • 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.
  • it has the structure connected through an electrolyte layer and accommodated in a battery case.
  • a battery using a material that is alloyed with Li for the negative electrode is expected as a negative electrode material for vehicle use because the energy density is improved as compared with a conventional carbon / graphite negative electrode material.
  • 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.
  • the volume expansion is about 1.2 times in graphite materials
  • Si materials when Si and Li are alloyed, transition from the amorphous state to the crystalline state causes a large volume change. (Approximately 4 times), there was a problem of reducing the cycle life of the electrode.
  • the 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.
  • a negative electrode active material for a lithium ion secondary battery including an amorphous alloy having the formula: Si x M y Al z has been proposed (see, for example, Patent Document 1).
  • M represents Mn, Mo, Nb, W, Ta, Fe, Cu, It is a metal composed of at least one of Ti, V, Cr, Ni, Co, Zr, and Y.
  • paragraph “0018” describes that, by minimizing the content of metal M, a good cycle life is exhibited in addition to high capacity.
  • an object of the present invention is to provide a negative electrode for an electric device such as a Li ion secondary battery that maintains a high cycle characteristic and has a high initial capacity and a well-balanced characteristic.
  • the present inventors have conducted intensive research to solve the above problems. As a result, it has been found that the above problem can be solved by using a negative electrode using a negative electrode active material obtained by mixing a predetermined ternary Si alloy and a carbon-based material, and to complete the present invention. It came.
  • the present invention relates to a negative electrode for an electric device having a current collector and an electrode layer including a negative electrode active material, a conductive additive, and a binder disposed on the surface of the current collector.
  • the negative electrode active material has the following formula (1):
  • M is at least one metal selected from the group consisting of C, Nb, and combinations thereof.
  • A is an inevitable impurity.
  • x, y, z, and a represent mass% values, where 0 ⁇ x ⁇ 100, 0 ⁇ y ⁇ 100, 0 ⁇ z ⁇ 100, and 0 ⁇ a ⁇ 0.5.
  • X + y + z + a 100.
  • FIG. 1 is a schematic cross-sectional view schematically showing an outline of a laminated flat non-bipolar lithium ion secondary battery which is a typical embodiment of an electric device according to the present invention.
  • FIG. 1 is a perspective view schematically showing the appearance of a stacked flat lithium ion secondary battery that is a representative embodiment of an electric device according to the present invention.
  • the discharge capacity (mAhg) of the first cycle of the battery using each sample (sample numbers 1 to 33) performed in Reference Example A of the invention was plotted according to the color of the capacity (with light and shade).
  • FIG. 3 is a composition diagram of a Si—Al—C ternary alloy.
  • the discharge capacity retention rate (%) at the 50th cycle of the battery using each sample (sample numbers 1 to 33) performed in Reference Example A of the present invention is color-coded according to the magnitude of the discharge capacity retention rate (light / dark) 2 is a composition diagram of a plotted Si—Al—C ternary alloy.
  • FIG. 4 is a drawing in which the composition range of the Si—Al—C ternary alloy composition of FIG. 3 is color-coded (with shading) surrounded by the composition range of the Si—Al—C alloy sample of Reference Example A.
  • FIG. 5 is a drawing in which a preferred composition range of the Si—Al—C alloy sample of Reference Example A is color-coded (shaded) with the composition diagram of the Si—Al—C ternary alloy of FIG. .
  • composition diagram of the Si—Al—C ternary alloy in FIG. 4 a more preferable composition range of the Si—Al—C alloy sample of Reference Example A is color-coded (shaded) and enclosed. is there.
  • the particularly preferred composition range of the Si—Al—C alloy sample of Reference Example A is color-coded (with shading) and enclosed. is there.
  • a particularly preferred composition range is color-coded (shaded) and enclosed. is there.
  • Evaluation cell (CR 2032 type coin cell) using an evaluation electrode using the Si (58 wt%)-Al (38 wt%)-C (4 wt%) alloy obtained in Sample 7 of Reference Example A of the present invention as a negative electrode active material 1) All the charge / discharge curves from 1 to 50 cycles in FIG. FIG.
  • FIG. 11 is a plot of each example in the composition diagram of the Si—Al—Nb ternary alloy, 0.27 ⁇ Si (mass% / 100) ⁇ 1.00, 0.00 ⁇ Al (mass% / 100) ⁇ 0.73, 0.00 ⁇ Nb (mass% / 100) ⁇ 0.58.
  • FIG. 12 is a plot of each example in the composition diagram of the Si—Al—Nb ternary alloy, 0.47 ⁇ Si (mass% / 100) ⁇ 0.95, 0.02 ⁇ Al (mass% / 100) ⁇ 0.48, 0.01 ⁇ Nb (mass% / 100) ⁇ 0.23.
  • FIG. 12 is a plot of each example in the composition diagram of the Si—Al—Nb ternary alloy, 0.47 ⁇ Si (mass% / 100) ⁇ 0.95, 0.02 ⁇ Al (mass% / 100) ⁇ 0.48, 0.01 ⁇ Nb (mass% / 100) ⁇ 0.23.
  • the present invention uses a negative electrode using a negative active material obtained by mixing a predetermined ternary Si alloy (ternary Si-Al-M alloy) and a carbon-based material. It is characterized in that
  • the negative electrode for an electric device according to the present invention when Si and Li are alloyed, by applying a ternary Si-Al-M alloy, the amorphous-crystal phase transition is suppressed and the cycle life is improved. Is obtained. Furthermore, by mixing the alloy and the graphite material, it is possible to prevent the occurrence of non-uniformity of reaction with the Li ions of the Si alloy in the electrode layer (negative electrode active material layer) and to improve cycle durability. can get. As a result of such combined action, the negative electrode for an electric device according to the present invention has a high initial capacity, and has a useful effect of having high capacity and high cycle durability.
  • electrode layer means a mixture layer containing a negative electrode active material, a conductive additive, and a binder, but may be referred to as a “negative electrode active material layer” in the description of this specification.
  • electrode layer on the positive electrode side is also referred to as a “positive electrode active material layer”.
  • the voltage of the cell is large. High energy density and high power density can be achieved. Therefore, the lithium ion secondary battery using the negative electrode for 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.
  • the present invention can be sufficiently applied to lithium ion secondary batteries for portable devices such as mobile phones.
  • the lithium ion secondary battery that is the subject of the present embodiment only needs to use the negative electrode for the lithium ion secondary battery of the present embodiment described below. It should not be restricted.
  • the lithium ion secondary battery when distinguished by form / structure, it can be applied to any conventionally known form / structure such as a stacked (flat) battery or a wound (cylindrical) battery. Is.
  • a stacked (flat) battery structure 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.
  • 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 a gel electrolyte) and a solid polymer (all solid) type battery using a polymer solid electrolyte (also simply referred to as a polymer electrolyte). It is done.
  • the non-bipolar (internal parallel connection type) lithium ion secondary battery using the negative electrode for the lithium ion secondary battery of this embodiment will be described very simply with reference to the drawings.
  • the technical scope of the lithium ion secondary battery of the present embodiment should not be limited to these.
  • 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.
  • stacked battery a flat (stacked) lithium ion secondary battery
  • 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.
  • 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. .
  • 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.
  • 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 described above is characterized by a negative electrode.
  • main components of the battery including the negative electrode will be described.
  • the active material layer 13 or 15 contains an active material, and further contains other additives as necessary.
  • the positive electrode active material layer 13 includes a positive electrode active material.
  • Positive electrode active material examples include lithium-transition metal composite oxides, lithium-transition metal phosphate compounds, lithium-transition metal sulfate compounds, solid solution systems, ternary systems, NiMn systems, NiCo systems, and spinel Mn systems. It is done.
  • lithium-transition metal composite oxide examples include LiMn 2 O 4 , LiCoO 2 , LiNiO 2 , Li (Ni, Mn, Co) O 2 , Li (Li, Ni, Mn, Co) O 2 , LiFePO 4 and Examples include those in which some of these transition metals are substituted with other elements.
  • Examples of the ternary system include nickel / cobalt / manganese (composite) cathode materials.
  • NiMn system examples include LiNi 0.5 Mn 1.5 O 4 .
  • NiCo system examples include Li (NiCo) O 2 .
  • Examples of the spinel Mn system include LiMn 2 O 4 .
  • two or more positive electrode active materials may be used in combination.
  • a lithium-transition metal composite oxide is used as the positive electrode active material.
  • positive electrode active materials other than those described above may be used.
  • 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.
  • the average particle diameter of the positive electrode active material contained in the positive electrode active material layer 13 is not particularly limited, but is preferably 1 to 30 ⁇ m and more preferably 5 to 20 ⁇ m from the viewpoint of increasing the output.
  • 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.
  • the value of “average particle diameter” is the value of particles observed in several to several tens of fields using 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.
  • 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.
  • the negative electrode active material layer 15 includes a negative electrode active material.
  • the negative electrode active material is a mixture of a predetermined alloy and a carbon-based material.
  • alloy is represented by the following chemical formula (1).
  • M is at least one metal selected from the group consisting of C, Nb, and combinations thereof.
  • A is an inevitable impurity.
  • x, y, z, and a represent mass% values, where 0 ⁇ x ⁇ 100, 0 ⁇ y ⁇ 100, 0 ⁇ z ⁇ 100, and 0 ⁇ a ⁇ 0.5.
  • X + y + z + a 100.
  • the “inevitable impurity” means an Si alloy that is present in a raw material or inevitably mixed in a manufacturing process. The inevitable impurities are originally unnecessary impurities, but are a very small amount and do not affect the characteristics of the Si alloy.
  • the first additive element Al and the second additive element M are selected as the negative electrode active material.
  • the cycle life can be improved by suppressing the phase transition of the amorphous-crystal during the Li alloying.
  • This also makes the capacity higher than that of a conventional negative electrode active material, for example, a carbon-based negative electrode active material.
  • the amorphous-crystal phase transition is suppressed because, in the Si material, when Si and Li are alloyed, the amorphous state transitions to the crystalline state, causing a large volume change (about 4 times). For this reason, the particles themselves are broken and the function as the active material is lost. Therefore, by suppressing the amorphous-crystal phase transition, it is possible to suppress the collapse of the particles themselves, maintain the function as the active material (high capacity), and improve the cycle life.
  • a Si alloy negative electrode active material having a high capacity and high cycle durability can be provided.
  • M is at least one metal selected from the group consisting of C, Nb, and combinations thereof. Therefore, hereinafter, Si x Al y C z A a and Si x Al y Nb z A a Si alloys will be described.
  • the Si x Al y C z A a is selected from Al as the first additive element and C as the second additive element, so that an amorphous-crystalline phase can be formed during Li alloying.
  • the cycle life can be improved by suppressing the transition. This also makes the capacity higher than that of a conventional negative electrode active material, for example, a carbon-based negative electrode active material.
  • the composition ratio of the Si—Al—C alloy is within the range surrounded by the thick solid line in FIG. 5 (inside the triangle), the composition ratio is extremely high that cannot be realized with an existing carbon-based negative electrode active material. High capacity can be realized. Similarly, even if compared with the existing Sn-based alloy negative electrode active material, the initial capacity is higher (initial capacity 1113 mAh / g or more), the capacity can be increased, and high initial charge / discharge efficiency (94% or more) can be realized.
  • the x, y, and z are represented by the following formula (2):
  • the Si alloy negative electrode active material having better characteristics can be obtained. Can provide material. Specifically, even when the composition ratio of the Si—Al—C alloy is within the range surrounded by the thick solid line in FIG. 6 (inside the hexagon in FIG. 6), it cannot be realized with the existing carbon-based negative electrode active material. A much higher capacity can be achieved.
  • the initial capacity is higher (initial capacity 1113 mAh / g or more), the capacity can be increased, and high initial charge / discharge efficiency (94% or more) can be realized.
  • the x, y, and z are represented by the following formula (3):
  • the Si alloy negative electrode active material having better characteristics can be obtained. Can provide material. Specifically, even when the composition ratio of the Si—Al—C alloy is within the range surrounded by the thick solid line in FIG. 7 (inside the hexagon in FIG. 7), it cannot be realized with the existing carbon-based negative electrode active material. A much higher capacity can be achieved. Similarly, even when compared with the existing Sn-based alloy negative electrode active material, the initial capacity is higher (initial capacity 1133 mAh / g or more), the capacity can be increased, and high initial charge / discharge efficiency (94% or more) can be realized.
  • the x, y, and z are represented by the following formula (4):
  • the Si alloy negative electrode having particularly good characteristics when the composition ratio of Al as the first additive element, C as the second additive element, and the high-capacity element Si is within the appropriate range specified above.
  • An active material can be provided. Specifically, even when the composition ratio of the Si—Al—C alloy is within the range surrounded by the thick solid line in FIG. 8 (inside the small hexagon), it is not possible with the existing carbon-based negative electrode active material. High capacity can be realized. Similarly, even when compared with the existing Sn-based alloy negative electrode active material, the initial capacity is higher (initial capacity 1133 mAh / g or more), the capacity can be increased, and high initial charge / discharge efficiency (94% or more) can be realized.
  • the cycle durability that is in a trade-off relationship with the increase in capacity, when compared with the Sn-based negative electrode active material having a high capacity but poor cycle durability and the multi-component alloy negative electrode active material described in Patent Document 1, Can realize extremely excellent cycle durability. Specifically, a high discharge capacity retention ratio of 74% or more at the 50th cycle can be realized. In other words, in this case, among the samples 1 to 18 of Reference Example A, the composition range in which the initial capacity is high and the capacity can be increased, the initial charge / discharge efficiency is high, and the cycle durability can be realized in a very balanced manner. Selected (small hexagon surrounded by thick solid line in FIG. 8). Thereby, a higher performance Si alloy negative electrode active material can be provided (refer to Table 1 and FIGS. 3, 4, and 8).
  • the x, y, and z are represented by the following formula (5):
  • the Si alloy negative electrode having the best characteristics when the composition ratio of the first additive element Al and the second additive element C, and the high-capacity element Si is within the appropriate range specified above.
  • An active material can be provided. Specifically, when the composition ratio of the Si—Al—C alloy is within the range surrounded by the thick solid line in FIG. 9 (inside the smallest hexagon), it cannot be realized with the existing carbon-based negative electrode active material. A much higher capacity can be achieved. Similarly, even if compared with the existing Sn-based alloy negative electrode active material, the initial capacity is higher (initial capacity 1192 mAh / g or more), the capacity can be increased, and high initial charge / discharge efficiency (97% or more) can be realized.
  • a very high performance Si alloy negative electrode active material can be provided (refer to Table 1 and FIGS. 3, 4 and 9).
  • the negative electrode active material in the production state (uncharged state), a ternary amorphous alloy represented by Si x Al y C z (A a) having an appropriate composition ratio described above. And in the lithium ion secondary battery using the negative electrode active material of this embodiment, even when Si and Li are alloyed by charging / discharging, it is possible to suppress the transition from the amorphous state to the crystalline state and cause a large volume change. It has remarkable characteristics that can be achieved.
  • the cycle characteristics are very poor and sufficient when compared with the discharge capacity retention ratio (about 60%) of the 50th cycle of the Sn-based negative electrode active material that can be increased in capacity to about 600 to 700 mAh / g.
  • the balance between the increase in capacity and the cycle durability, which are in a trade-off relationship, is poor and cannot be put into practical use.
  • the quaternary alloy of Si 62 Al 18 Fe 16 Zr 4 in Example 1 of Patent Document 1 has an initial capacity as high as about 1150 mAh / g from FIG. 2, but only 5 to 6 cycles. It is shown that the later circulation capacity is already only about 1090 mAh / g.
  • the initial capacity is as high as about 1430 mAh / g from FIG. 4, but the circulation capacity after only 5 to 6 cycles is It has already been shown that it has already greatly decreased to about 1300 mAh / g.
  • the quaternary alloy of Si 60 Al 20 Fe 12 Ti 8 of Example 3 and the quaternary alloy of Si 62 Al 16 Fe 14 Ti 8 of Example 4 there is no description of the initial capacity. It is shown that the circulating capacity after ⁇ 6 cycles has already become a low value of 700 to 1200 mAh / g.
  • the alloy composition of patent document 1 is described by atomic ratio, when converted into mass ratio like this embodiment, about 20 mass% of Fe is contained in the Example, and it becomes a 1st addition element. It can be said that the alloy composition is disclosed.
  • batteries using these binary alloys or ternary or quaternary alloys described in Patent Document 1 have cycle characteristics that satisfy a practical level in fields where cycle durability is strongly required, such as in vehicles. There are problems in its reliability and safety, such as insufficient availability, making it difficult to put it to practical use.
  • the negative electrode active material using a ternary alloy represented by the present embodiment Si x Al y C z (A a) has a high discharge capacity maintenance ratio of the 50th cycle as high cycle characteristics (FIG. 7 To 9).
  • the initial capacity (discharge capacity at the first cycle) is also significantly higher than that of the existing carbon-based negative electrode active material, and is equal to or higher than that of the existing Sn-based negative electrode active material (see Table 1 and FIG. 3).
  • a negative electrode active material having high initial charge / discharge efficiency and exhibiting well-balanced characteristics can be provided.
  • further initial The present inventors have found a negative electrode active material using an alloy that can achieve charge / discharge efficiency in a high-order and well-balanced manner.
  • two types of Al and C are selected from the group consisting of one or two or more additive element species in which there are very various combinations, and a specific composition of these additive element species and high-capacity element Si is selected. It has been found that the intended purpose can be achieved by selecting the ratio (composition range). As a result, it is excellent in that it can provide a lithium ion secondary battery that has a higher initial capacity, a higher capacity, a higher initial charge / discharge efficiency, and a higher balance in cycle durability.
  • anode active material Si x Al y C z A a Will be described in more detail below the anode active material Si x Al y C z A a .
  • the range of x is preferably 36 ⁇ x ⁇ 100 More preferably, 36 ⁇ x ⁇ 80, still more preferably 41 ⁇ x ⁇ 71, and particularly preferably 43 ⁇ x ⁇ 61.
  • the mass% value (x value) of the high-capacity element Si in the alloy preferably maintains a high cycle characteristic (a high discharge capacity retention rate at the 50th cycle) while maintaining a high balance between the initial capacity and the high charge / discharge efficiency.
  • the range of 36 ⁇ x ⁇ 80 is desirable from the viewpoint of providing the negative electrode active material shown.
  • the composition ratio of Al as the first additive element and C in the second additive element is appropriate, good characteristics (high capacity and cycle that are in a trade-off relationship with existing alloy negative electrode active materials) It is possible to realize a Si alloy negative electrode active material having durability and characteristics excellent in charge / discharge efficiency.
  • the mass% value (x value) of the high-capacity element Si in the alloy exhibits a high balance between the high initial capacity and the high charge / discharge efficiency while maintaining higher cycle characteristics (higher discharge capacity retention ratio).
  • the range of 41 ⁇ x ⁇ 71 is more desirable.
  • a Si alloy negative electrode active material having better characteristics can be provided (Table 1 and FIG.
  • the mass% value (x value) of the high-capacity element Si in the alloy is particularly preferably a balance between high initial capacity and high charge / discharge efficiency while maintaining particularly high cycle characteristics (particularly high discharge capacity retention). From the viewpoint of providing a negative electrode active material, the range of 43 ⁇ x ⁇ 61 is particularly desirable.
  • a high-performance Si alloy negative electrode active material having the best characteristics can be provided when the ratio of Al, which is the first additive element, and C of the second additive element, which will be described later, is more appropriate (Table 1). 1 and the internal reference surrounded by the thick solid line in FIG. 9).
  • the capacity is high (1192 mAh / g or more), high charge / discharge efficiency (97% or more), and particularly high discharge capacity maintenance ratio (81 in the 50th cycle) (81 % Or more) can be maintained (internal reference enclosed by a thick solid line in Table 1 and FIG. 9).
  • the content ratio (balance) of Si material having an initial capacity of 3200 mAh / g, Al as the first additive element, and C as the second additive element is optimal. (See the range surrounded by the thick solid line in FIGS. 7 to 9). Therefore, it is excellent in that the most favorable characteristics can be expressed and the increase in capacity at the vehicle application level can be stably and safely maintained over a long period of time.
  • x ⁇ 71, particularly x ⁇ 61 the high content Si material having an initial capacity of 3200 mAh / g and the content ratio (balance) of the first additive element Al and the second additive element C are optimal.
  • Patent Document 1 it is disclosed in the above-mentioned embodiment of Patent Document 1 that the degradation of cycle characteristics due to a considerable capacity reduction is already exhibited in only about 5 to 6 cycles. That is, in the example of Patent Document 1, the discharge capacity maintenance rate at the 5th to 6th cycles has already been reduced to 90 to 95%, and the discharge capacity maintenance rate at the 50th cycle has been reduced to almost 50 to 0%. It will be.
  • the combination of the first additive element Al and the second additive element C to Si is mutually complementary, so to speak, many trials and errors, and various combinations of additive (metal or nonmetal) elements. It was possible to select through an excessive experiment.
  • the reduction in the discharge capacity maintenance ratio and the initial charge / discharge efficiency at the 50th cycle is greatly reduced along with the increase in capacity. It is also excellent in that it can be done. That is, when Si and Li are alloyed, the crystal is crystallized from an amorphous state by a particularly remarkable synergistic effect (effect) due to the optimum range of the first additive element Al and the second additive element C mutually complementary to the Al. The transition to the state can be suppressed, and a large volume change can be prevented. Furthermore, it is excellent also in that the high cycle durability of the electrode can be improved while showing a high capacity.
  • the range of y that is the mass% value of Al in the alloy having the composition formula Si x Al y C z A a is preferably 0 ⁇ y ⁇ 64, More preferably, 10 ⁇ y ⁇ 56, still more preferably 15 ⁇ y ⁇ 56, and particularly preferably 20 ⁇ y ⁇ 54. This is because if the numerical value of the mass percentage (y value) of the first additive element Al in which the capacity as an electrode does not decrease even if the concentration of C in the alloy increases, the value of C Due to the synergistic characteristics of Al and Al, the amorphous-crystal phase transition of the high-capacity Si material can be effectively suppressed.
  • the initial capacity is high, the capacity can be increased, the initial charge / discharge efficiency is high, and an effect excellent in cycle life (cycle durability) can be exhibited.
  • a high initial capacity of 1113 mAh / g or higher, particularly 1133 mAh / g or higher, particularly 1192 mAh / g or higher can exhibit a high initial charge / discharge efficiency of 94% or higher, particularly 97% or higher.
  • a high discharge capacity retention rate at the 50th cycle 64% or more, particularly 74% or more, particularly 81% or more can be exhibited (see Table 1, FIGS. 7 to 9).
  • the content x value of the high-capacity Si material can be maintained at a certain value (36 ⁇ x ⁇ 100), and the capacity can be increased significantly, which cannot be realized with existing carbon-based negative electrode active materials. realizable. Similarly, even when compared with the existing Sn-based alloy negative electrode active material, a higher capacity alloy can be obtained.
  • the mass% value (y value) of the first additive element Al in the alloy is preferably 10 from the viewpoint of providing a negative electrode active material that exhibits a high balance between high cycle characteristics and high initial capacity and high initial charge / discharge efficiency.
  • a range of ⁇ y ⁇ 56 is desirable.
  • the capacity of the second additive element C which suppresses the amorphous-crystal phase transition and improves the cycle life, and the negative electrode active material (negative electrode) does not decrease even when the concentration of the second additive element increases. Selection of the first additive element Al is extremely important and useful in the present embodiment.
  • first and second additive elements With such first and second additive elements, a known ternary alloy, a quaternary or higher alloy such as Patent Document 1, and a binary alloy such as a Si—C alloy or Si—Al alloy can be used. It was found that there was a significant difference in action and effect.
  • the Si alloy negative electrode active material having good characteristics is obtained (Table 1 and FIG. 7). (See composition range surrounded by thick solid line).
  • the numerical value of the mass% value (y value) of the first additive element Al in the alloy is 10 ⁇ y ⁇ 56 in the preferred range, due to the synergistic effect (mutual complementary characteristics) with the second additive element C, When alloying, the effect of suppressing the amorphous-crystal phase transition and improving the cycle life can be effectively expressed.
  • the initial capacity is high, the capacity can be increased, the initial charge / discharge efficiency is high, and an effect excellent in cycle life (cycle durability) can be exhibited.
  • an excellent effect of a high initial charge / discharge efficiency of 94% or more can be exhibited at a high initial capacity of 1113 mAh / g or more, particularly 1133 mAh / g or more.
  • the mass% value (y value) of the first additive element Al in the alloy is particularly preferably 15 from the viewpoint of providing a negative electrode active material having a higher balance between high cycle characteristics and high initial capacity and initial charge / discharge efficiency.
  • a range of ⁇ y ⁇ 56 is desirable.
  • the initial capacity is high, the capacity can be increased, the initial charge / discharge efficiency is high, and an effect excellent in cycle life (cycle durability) can be exhibited.
  • an excellent effect of high initial charge / discharge efficiency of 94% or more can be exhibited at a high initial capacity of 1133 mAh / g or more.
  • an excellent effect of a high discharge capacity retention ratio of 74% or more at the 50th cycle can be exhibited (see Table 1 and FIG. 8).
  • the composition range (especially containing Al) can achieve higher capacity, and can realize higher initial charge / discharge efficiency and better cycle life (cycle durability).
  • the amount 15 ⁇ y ⁇ 56 is selected. That is, the composition range is inside a small hexagon surrounded by a thick solid line in FIG.
  • 15 ⁇ y ⁇ 56 for the composition range, particularly the Al content the synergistic effect with C increases the capacity, as well as the existing high capacity Sn-based negative electrode active materials and the multiple elements described in Patent Document 1.
  • the negative electrode-based alloy negative electrode active material it is possible to realize remarkably excellent cycle durability.
  • a well-balanced Si alloy negative electrode active material that realizes a discharge capacity retention ratio of 64% or more at the 50th cycle can be provided.
  • the mass% value (y value) of the first additive element Al in the alloy is particularly preferable from the viewpoint of providing a negative electrode active material that exhibits the best balance between higher cycle characteristics and higher initial capacity and higher initial charge / discharge efficiency.
  • a range of 20 ⁇ y ⁇ 54 is desirable.
  • the Si alloy negative electrode active material having the best characteristics can be provided.
  • the amorphous-crystal phase transition can be more effectively suppressed during alloying due to a synergistic effect with C (mutual complementarity).
  • C partial complementarity
  • the initial capacity is high, the capacity can be increased, the initial charge / discharge efficiency is high, and an effect excellent in cycle life (cycle durability) can be exhibited.
  • an excellent effect of high initial charge / discharge efficiency of 97% or higher can be exhibited at a high initial capacity of 1192 mAh / g or higher.
  • the outstanding effect of the high discharge capacity maintenance factor 81% or more in 50th cycle can also be expressed (refer Table 1, FIG. 9).
  • the composition range (especially containing Al) can achieve higher capacity, and can realize higher initial charge / discharge efficiency and better cycle life (cycle durability).
  • 20 ⁇ y ⁇ 54 is selected. That is, the composition range within the smallest hexagon surrounded by the thick solid line in FIG.
  • 20 ⁇ y ⁇ 54 with respect to the composition range, particularly the Al content, a synergistic effect with C can increase the capacity, as well as the existing high capacity Sn-based negative electrode active material and Patent Document 1 Even when compared with the multi-component alloy negative electrode active material, it is possible to provide a well-balanced Si alloy negative electrode active material that realizes excellent cycle durability and initial charge / discharge efficiency.
  • the composition formula Si x Al y C z (A a) adding a metal element of the ternary system to the Si alloy represented by (Al, C) 2 ternary alloy does not contain one of (especially, High cycle characteristics and charge / discharge efficiency cannot be maintained with a Y—Si—C alloy).
  • the high discharge capacity maintenance rate and the high initial charge / discharge efficiency at the 50th cycle cannot be maintained, and the initial charge / discharge efficiency is reduced or the cycle characteristics are deteriorated (deteriorated). Therefore, it has not been possible to provide a Si alloy negative electrode active material that achieves the best balance between the above-described excellent cycle durability and high initial capacity and charge / discharge efficiency.
  • the high-capacity Si material having the initial capacity of 3200 mAh / g, the first additive element Al, and the further second additive element C The content ratio (balance) can be in an optimum range (see the range surrounded by the thick solid line in FIGS. 7 to 9). Therefore, even if the C concentration that can suppress the amorphous-crystal phase transition, which is a characteristic of Al, increases, the capacity decrease as the negative electrode active material (negative electrode) is effectively suppressed. Life (especially discharge capacity maintenance rate) and charge / discharge efficiency can be significantly improved.
  • the negative electrode active material (negative electrode) is excellent in that it can exhibit the best characteristics and can maintain a high capacity at the vehicle application level stably and safely over a long period of time.
  • the content ratio of the high-capacity Si material having an initial capacity of about 3200 mAh / g, the first additive element Al, and the second additive element C (Balance) can be an optimum range (see the range surrounded by a thick solid line in FIGS. 7 to 9).
  • the amorphous-crystal phase transition can be remarkably suppressed, and the cycle life (particularly the discharge capacity retention rate) and charge / discharge efficiency can be greatly improved along with the increase in capacity. . That is, a high initial capacity of 1133 mAh / g or more, particularly 1192 mAh / g or more can be realized, and a high initial charge / discharge efficiency of 94% or more, particularly 97% or more can be realized. Further, a high discharge capacity retention ratio of 64% or more, particularly 74% or more, particularly 81% or more can be realized at the 50th cycle.
  • Patent Document 1 it is disclosed in the above-mentioned embodiment of Patent Document 1 that the degradation of cycle characteristics due to a considerable capacity reduction is already exhibited in only about 5 to 6 cycles. That is, in the example of Patent Document 1, the discharge capacity maintenance rate at the 5th to 6th cycles has already been reduced to 90 to 95%, and the discharge capacity maintenance rate at the 50th cycle has been reduced to almost 50 to 0%. It will be.
  • the combination of the first additive element Al and the second additive element C to the high-capacity Si material has a mutually complementary relationship, so to speak, many trials and errors, and various additions (metal or non-additional). It can be selected through an excessive experiment with a combination of (metal) elements (only one combination).
  • the range of z is the mass percent of C in the alloy with C mass%
  • the above composition formula for values Si x Al y C z A a of the alloy is preferably 0 ⁇ z ⁇ 64, More preferably, 3 ⁇ z ⁇ 37, and further preferably 3 ⁇ z ⁇ 29. This is because, if the numerical value of the mass% value (z value) of the second additive element species C in the alloy is in the range of 0 ⁇ z ⁇ 64, the high capacity Si due to the characteristics of C and the synergistic characteristics with Al. The amorphous-crystal phase transition of the material can be effectively suppressed.
  • an alloy having a higher capacity (initial capacity 1113 mAh / g or more, particularly 1133 mAh / g or more, especially 1192 mAh / g or more) can be obtained even when compared with existing Sn-based negative electrode active materials (Table 1 and FIG. 5-8).
  • the mass% value (z value) of the second additive element C in the alloy maintains a high cycle characteristic (a high discharge capacity retention ratio at the 50th cycle), and a balance between a high initial capacity and a high initial charge / discharge efficiency.
  • a range of 3 ⁇ z ⁇ 37 is desirable.
  • the value of the mass% (z value) of the second additive element C in the alloy is 3 ⁇ z ⁇ 37, which is a preferable range, the amorphous-crystal phase transition is suppressed during alloying and the cycle life is reduced. It is preferable at the point which can effectively express the effect which improves.
  • the composition range (especially with respect to the C content) in which high capacity (1113 mAh / g or more) and high initial charge / discharge efficiency (94% or more) could be realized with Samples 1 to 18 of Reference Example A. (3 ⁇ z ⁇ 37) is selected (a hexagon surrounded by a thick solid line in FIG. 6).
  • the initial charge / discharge efficiency is higher than that of the existing Sn-based negative electrode active material and the multi-component alloy negative electrode active material described in Patent Document 1.
  • Si alloy negative electrode active material realizing cycle durability.
  • the initial capacity and the initial charge / discharge efficiency are also maintained while maintaining higher cycle characteristics (high discharge capacity retention rate at the 50th cycle).
  • the range of 3 ⁇ z ⁇ 29 is desirable from the viewpoint of providing a negative electrode active material exhibiting the highest balance of high characteristics.
  • the Si alloy negative electrode active material having the best characteristics is most suitable. Substances can be provided (see Table 1 and Figures 7-9).
  • the composition range (particularly C) that can achieve higher capacity, higher initial charge / discharge efficiency, and higher discharge capacity retention ratio at the 50th cycle was selected (hexagons surrounded by thick solid lines in FIGS. 7 to 9).
  • 3 ⁇ z ⁇ 29 for the above composition range, particularly C content with excellent cycle durability compared to the Sn-based negative electrode active material and the multi-component alloy negative electrode active material described in Patent Document 1, It is possible to provide a Si alloy negative electrode active material that achieves the most balanced characteristics with high initial capacity and charge / discharge efficiency.
  • the composition formula Si x Al y C z (A a) adding a metal element to Si respect ternary alloy represented by (Al, C) 2 ternary alloy does not contain one of (
  • the high discharge capacity maintenance rate and the high initial charge / discharge efficiency at the 50th cycle cannot be maintained, and the initial charge / discharge efficiency is reduced or the cycle characteristics are deteriorated (deteriorated). Therefore, it has not been possible to provide a Si alloy negative electrode active material that achieves the best balance between the above-described excellent cycle durability and high initial capacity and charge / discharge efficiency.
  • the content ratio of the high-capacity Si material having the initial capacity of 3200 mAh / g and the first additive element Al and the second additive element C (Balance) can be in an optimal range (see the range surrounded by the thick solid line in FIGS. 7 to 9). Therefore, it effectively suppresses the amorphous-crystal phase transition of the Si material, which is a characteristic of C (and also a synergistic characteristic with Al), increases the capacity, as well as the cycle life (especially the discharge capacity maintenance rate) and charge. Discharge efficiency can be significantly improved.
  • the negative electrode active material (negative electrode) is excellent in that it can exhibit better characteristics and can maintain a high capacity at the vehicle application level stably and safely over a long period of time.
  • z ⁇ 29 C content is 29 mass% or less
  • the content ratio (balance) of C can be in an optimum range (see the range surrounded by the thick solid line in FIGS. 7 to 9). Therefore, when alloying Si and Li, the amorphous-crystal phase transition can be remarkably suppressed, and the cycle life can be greatly improved.
  • a high initial capacity of 1133 mAh / g or more, particularly 1192 mAh / g or more can be realized, and a high initial charge / discharge efficiency of 94% or more, particularly 97% or more can be realized.
  • a high discharge capacity retention ratio of 64% or more, particularly 74% or more, particularly 81% or more can be realized at the 50th cycle.
  • z is outside the above optimal range (3 ⁇ z ⁇ 29)
  • Patent Document 1 it is disclosed in the above-mentioned embodiment of Patent Document 1 that the degradation of cycle characteristics due to a considerable capacity reduction is already exhibited in only about 5 to 6 cycles. That is, in the example of Patent Document 1, the discharge capacity maintenance rate at the 5th to 6th cycles has already been reduced to 90 to 95%, and the discharge capacity maintenance rate at the 50th cycle has been reduced to almost 50 to 0%. It will be.
  • the combination of the first additive element Al and the second additive element C to the high-capacity Si material is mutually complementary, so to speak, many trials and errors and various additions (metal or nonmetal). It can be selected through an excessive experiment with combinations of elemental species (only one combination).
  • the content of C is further in the optimum range shown above, it is also excellent in that the decrease in the discharge capacity maintenance rate at the 50th cycle can be greatly reduced. That is, when Si and Li are alloyed, the crystalline state is changed from an amorphous state by a particularly remarkable synergistic effect (effect) due to the optimum range of the first additive element Al and further the second additive element C mutually complementary to Al. Can be prevented and a large volume change can be prevented. Furthermore, it is excellent in that the high cycle durability and the initial charge / discharge efficiency of the electrode can be improved while showing a high capacity (see Table 1 and FIGS. 7 to 9).
  • Range of a a weight percent of A in the alloy having the above composition formula Si x Al y C z A a for mass% value of A in the alloy is 0 ⁇ a ⁇ 0.5, More preferably, 0 ⁇ x ⁇ 0.1.
  • A is present in the raw material in the Si alloy or is inevitably mixed in the manufacturing process, and is originally unnecessary, but it is a trace amount and affects the characteristics of the Si alloy. Therefore, it is allowed to be contained in the alloy.
  • the Si x Al y Nb z A a is selected from Al as the first additive element and Nb as the second additive element.
  • the cycle life can be improved by suppressing the transition. This also makes the capacity higher than that of a conventional negative electrode active material, for example, a carbon-based negative electrode active material.
  • Such a negative electrode active material can exhibit excellent cycle characteristics while maintaining a high discharge capacity as compared with a carbon-based negative electrode active material having a charge / discharge capacity of about 300 mAh / g. It is suitably used for a negative electrode. As a result, it can be suitably used as a lithium-ion secondary battery for vehicle drive power or auxiliary power. In addition to this, the present invention can be sufficiently applied to lithium ion secondary batteries for portable devices such as mobile phones.
  • the alloy absorbs lithium ions during charge / discharge of the battery and releases lithium ions during discharge.
  • the negative electrode active material is a Si alloy negative electrode active material, and includes a first additive element that suppresses amorphous-crystal phase transition and improves cycle life when alloyed with lithium by charging. It contains some Al, and further contains Nb as a second additive element that makes it difficult to reduce the capacity as an electrode even if the concentration of the first additive element increases. As a result, high capacity and high cycle durability can be exhibited, and further high charge / discharge efficiency can be exhibited in the initial stage.
  • the negative electrode active material made of a Si—Al—Nb-based alloy if the x exceeds 27, a sufficient initial capacity can be obtained. If x is less than 100, cycle characteristics improved over conventional pure silicon can be obtained. In addition, when y exceeds 0, cycle characteristics improved over pure silicon are obtained, and when y is less than 73, the silicon content is relatively high, so that the initial capacity is the existing capacity. There is a tendency to be improved as compared with the negative electrode active material. When z exceeds 0, cycle characteristics improved over pure silicon are obtained, and when z is less than 58, the silicon content is relatively high, so that the initial capacity is less than the existing negative electrode active capacity. There is a tendency to improve compared to substances.
  • 61 ⁇ x ⁇ 84, 2 ⁇ y ⁇ 25, and 2 ⁇ z ⁇ 23 are preferable. This numerical range corresponds to the range indicated by the symbol C in FIG.
  • A is an impurity (unavoidable impurity) other than the above three components derived from the raw materials and the manufacturing method.
  • the a is 0 ⁇ a ⁇ 0.5, and more preferably 0 ⁇ a ⁇ 0.1.
  • the average particle diameter of the Si alloy is not particularly limited as long as it is approximately the same as the average particle diameter of the negative electrode active material included in the existing negative electrode active material layer 15. From the viewpoint of higher output, it is preferably in the range of 1 to 20 ⁇ m. 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 the Si alloy is not particularly limited, and may be spherical, elliptical, cylindrical, polygonal, scaly, indeterminate, or the like.
  • a method for producing an alloy having a composition formula Si x Al y M z A a according to the manufacturing method according to this embodiment of the alloy is not limited in particular, can be produced by utilizing the production of conventionally known various . That is, since there is almost no difference in the alloy state and characteristics depending on the production method, various production methods can be applied.
  • a mechanical alloy method, an arc plasma melting method, or the like can be used as a method for producing a particle form of an alloy having the composition formula Si x Al y M z A a .
  • a slurry in the method of manufacturing in the form of the above particles, can be prepared by adding a binder, a conductive additive and a viscosity adjusting solvent to the particles, and a slurry electrode can be formed using the slurry. Therefore, it is excellent in that it is easy to mass-produce (mass production) and to be practically used as an actual battery electrode.
  • Carbon-based material The carbon-based material that can be used in the present invention is not particularly limited, but is graphite (graphite) that is highly crystalline carbon such as natural graphite or artificial graphite; low-crystalline carbon such as soft carbon or hard carbon; Carbon black such as chain black, acetylene 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.
  • graphite graphite
  • highly crystalline carbon such as natural graphite or artificial graphite
  • low-crystalline carbon such as soft carbon or hard carbon
  • Carbon black such as chain black, acetylene black, channel black, lamp black, oil furnace black, and thermal black
  • carbon materials such as fullerene, carbon nanotube, carbon nanofiber, carbon nanohorn, and carbon fibril.
  • graphite is preferably used.
  • the negative electrode active material is mixed with a carbon-based material together with the above alloy, so that it is possible to maintain a high cycle characteristic and to have a high initial capacity and a well-balanced characteristic.
  • the Si alloy may not be uniformly arranged in the negative electrode active material layer. In such a case, the electric potential and capacity which each Si alloy expresses differ individually. As a result, in the Si alloy in the negative electrode active material layer, a Si alloy that reacts excessively with Li ions and a Si alloy that does not react with Li ions are generated. That is, non-uniformity of reaction with Li ions of the Si alloy in the negative electrode active material layer occurs. Then, among the above alloys, the Si alloy that reacts with Li ions excessively acts, so that the decomposition of the electrolytic solution due to a significant reaction with the electrolytic solution and the destruction of the structure of the Si alloy due to excessive expansion may occur. As a result, even when a Si alloy having excellent characteristics is used, when the Si alloy is not uniformly disposed, the cycle characteristics can be deteriorated as a negative electrode for an electric device.
  • the above problem can be solved by mixing the Si alloy with a carbon-based material. More specifically, by mixing the Si alloy with the carbon-based material, it may be possible to uniformly dispose the Si alloy in the negative electrode active material layer. As a result, all of the Si alloys in the negative electrode active material layer exhibit the same reactivity, and can prevent deterioration of cycle characteristics.
  • the initial capacity can be reduced by reducing the content of the Si alloy in the negative electrode active material layer.
  • the carbon-based material itself has reactivity with Li 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.
  • the carbon-based material is unlikely to change in volume when reacting with Li ions as compared with the Si alloy. Therefore, even when the volume change of the Si alloy 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 Li 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 content of the carbonaceous material increases (the content of Si alloy decreases) (Table 3 and FIG. 14). See).
  • the amount of electricity consumed (Wh) can be improved by containing a carbon-based material. More specifically, the carbon-based material has a relatively low potential compared to the Si alloy. As a result, the relatively high potential of the Si alloy 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.
  • the shape of the carbon-based material is not particularly limited, and may be spherical, elliptical, cylindrical, polygonal, scaly, indefinite, or the like.
  • the average particle diameter of the carbon-based material is not particularly limited, but is preferably 5 to 25 ⁇ m, and more preferably 5 to 10 ⁇ m.
  • the average particle diameter of the carbon-based material may be the same as or different from the average particle diameter of the Si alloy. preferable.
  • the average particle size of the alloy is more preferably smaller than the average particle size of the carbonaceous material.
  • the ratio of the average particle size of the carbon-based material to the average particle size of the Si alloy is preferably 1/250 to less than 1, It is more preferably 1/100 to 1/4.
  • the mixing ratio of the Si alloy of the negative electrode active material and the carbon-based material is not particularly limited, and can be appropriately selected according to a desired application.
  • the content of the alloy in the negative electrode active material is preferably 3 to 70% by mass.
  • the content of the alloy in the negative electrode active material is more preferably 30 to 50% by mass.
  • the content of the alloy in the negative electrode active material is more preferably 50 to 70% by mass.
  • the content of the alloy is 3% by mass or more because a high initial capacity can be obtained.
  • the content of the alloy is 70% by mass or less, it is preferable because high cycle characteristics can be obtained.
  • the negative electrode active material is not particularly limited, and can be produced by a known method.
  • the negative electrode active material layer may use the above-described method for producing an alloy. Specifically, using a mechanical alloy method, an arc plasma melting method or the like to produce a Si alloy in a particle form, a slurry is prepared by adding a carbon-based material, a binder, a conductive additive, and a mucus modifier. A slurry electrode can be formed using the slurry. Under the present circumstances, the negative electrode active material from which Si alloy becomes desired content can be manufactured by changing suitably the quantity of Si alloy of a particle form, and the quantity of carbonaceous material.
  • the positive electrode active material layer 13 and the negative electrode active material layer 15 include a binder, a conductive additive, an electrolyte salt (lithium salt), an ion conductive polymer, and the like.
  • the binder used for the binder active material layer is not particularly limited, and examples thereof include the following materials. Polyethylene, polypropylene, polyethylene terephthalate (PET), polyether nitrile (PEN), polyacrylonitrile, polyimide, polyamide, polyamideimide, cellulose, carboxymethylcellulose (CMC), 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 Thermoplastic polymers such as hydrogenated products, polyvinylidene fluoride (PVdF), polytetrafluoroethylene (PT
  • polyvinylidene fluoride, polyimide, styrene / butadiene rubber, carboxymethyl cellulose, polypropylene, polytetrafluoroethylene, polyacrylonitrile, polyamide, and polyamideimide are more preferable, and polyamide is more preferable.
  • These suitable binders are excellent in heat resistance, have a very wide potential window, are stable at both the positive electrode potential and the negative electrode potential, and can be used for the active material layer. Further, a binder having a relatively strong binding force such as polyamide can favorably hold the Si alloy on the carbon-based material. These binders may be used alone or in combination of two.
  • the amount of the binder contained in the active material layer is not particularly limited as long as it is an amount capable of binding the active material, but is preferably 0.5 to 15% by mass with respect to the active material layer. More preferably, it is 1 to 10% by mass.
  • Conductive auxiliary agent means the additive mix
  • Examples of the conductive assistant include carbon materials such as carbon black such as acetylene black, graphite, and vapor grown carbon fiber.
  • the conductive binder having the functions of the conductive assistant and the binder may be used in place of the conductive assistant and the binder, or may be used in combination with one or both of the conductive assistant and the binder.
  • Commercially available TAB-2 (manufactured by Hosen Co., Ltd.) can be used as the conductive binder.
  • the content of the conductive additive mixed into the active material layer is in the range of 1% by mass or more, more preferably 3% by mass or more, and further preferably 5% by mass or more with respect to the total amount of the active material layer.
  • the content of the conductive additive mixed in the active material layer is 15% by mass or less, more preferably 10% by mass or less, and further preferably 7% by mass or less with respect to the total amount of the active material layer. is there.
  • Electrolyte salt lithium salt
  • 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.
  • Ion conductive polymer examples include polyethylene oxide (PEO) -based and polypropylene oxide (PPO) -based polymers.
  • the compounding ratio of the components contained in the negative electrode active material layer in the case of using the positive electrode active material layer and the alloy in the form of particles of (5) (ii) above is not particularly limited.
  • the mixing ratio can be adjusted by appropriately referring to known knowledge about the non-aqueous solvent secondary battery.
  • each active material layer (active material layer on one side of the current collector) is not particularly limited, and conventionally known knowledge about the battery can be appropriately referred to.
  • the thickness of each active material layer is usually about 1 to 500 ⁇ m, preferably 2 to 100 ⁇ m, taking into consideration the intended use of the battery (emphasis on output, energy, etc.) and ion conductivity.
  • the current collectors 11 and 12 are 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.
  • the thickness of the current collector is usually about 1 to 100 ⁇ m.
  • the shape of the current collector is not particularly limited.
  • a mesh shape (such as an expanded grid) can be used.
  • the negative electrode active material is formed directly on the negative electrode current collector 12 by sputtering or the like, it is desirable to use a current collector foil.
  • 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.
  • examples of the metal include aluminum, nickel, iron, stainless steel, titanium, and copper.
  • 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.
  • covered on the metal surface may be sufficient.
  • 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).
  • PE polyethylene
  • HDPE high density polyethylene
  • LDPE low density polyethylene
  • PP polypropylene
  • PET polyethylene terephthalate
  • PEN polyether nitrile
  • PI polyimide
  • PAI polyamideimide
  • PA polyamide
  • PTFE polytetraflu
  • a conductive filler may be added to the conductive polymer material or the non-conductive polymer material as necessary.
  • 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 has a conductivity.
  • metals, conductive carbon, etc. are mentioned as a material excellent in electroconductivity, electric potential resistance, or lithium ion barrier
  • 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.
  • 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 capable of imparting sufficient conductivity to the current collector, and is generally about 5 to 35% by mass.
  • a liquid electrolyte or a polymer electrolyte can be used as the electrolyte constituting the electrolyte layer 17.
  • the liquid electrolyte has a form in which a lithium salt (electrolyte salt) is dissolved in an organic solvent.
  • organic solvent include ethylene carbonate (EC), propylene carbonate (PC), butylene carbonate (BC), vinylene carbonate (VC), dimethyl carbonate (DMC), diethyl carbonate (DEC), ethyl methyl carbonate (EMC), Examples include carbonates such as methylpropyl carbonate (MPC).
  • Li (CF 3 SO 2) 2 N Li (C 2 F 5 SO 2) 2 N, LiPF 6, LiBF 4, LiAsF 6, LiTaF 6, LiClO 4, LiCF 3 SO 3 , etc.
  • a compound that can be added to the active material layer of the electrode can be employed.
  • polymer electrolytes are classified into gel electrolytes containing an electrolytic solution and intrinsic polymer electrolytes not containing an electrolytic solution.
  • the gel electrolyte has a configuration in which the above liquid electrolyte (electrolytic solution) is injected into a matrix 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 it is easy to block ion conduction between the layers.
  • Examples of the ion conductive polymer used as the matrix polymer include polyethylene oxide (PEO), polypropylene oxide (PPO), and copolymers thereof.
  • PEO polyethylene oxide
  • PPO polypropylene oxide
  • electrolyte salts such as lithium salts can be well dissolved.
  • the ratio of the liquid electrolyte (electrolytic solution) in the gel electrolyte is not particularly limited, but is preferably about several mass% to 98 mass% from the viewpoint of ionic conductivity.
  • the gel electrolyte having a large amount of electrolytic solution having a ratio of the electrolytic solution of 70% by mass or more is particularly effective.
  • a separator may be used for the electrolyte layer.
  • the separator include a microporous film made of polyolefin such as polyethylene and polypropylene, a porous flat plate, and a non-woven fabric.
  • the intrinsic polymer electrolyte has a structure in which a supporting salt (lithium salt) is dissolved in the above matrix polymer, and does not contain an organic solvent that is a plasticizer. Therefore, when the electrolyte layer is composed of an intrinsic polymer electrolyte, there is no fear of liquid leakage from the battery, and the reliability of the battery can be improved.
  • a supporting salt lithium salt
  • the matrix polymer of the gel electrolyte or the intrinsic polymer electrolyte can express excellent mechanical strength by forming 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.
  • a current collecting plate may be used for the purpose of taking out the current outside the battery.
  • the current collector plate is electrically connected to the current collector and the lead, and is taken out of the laminate sheet that is a battery exterior material.
  • the material constituting the current collector plate is not particularly limited, and a known highly conductive material conventionally used as a current collector plate for a lithium ion secondary battery can be used.
  • 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, and aluminum is more preferable from the viewpoint of light weight, corrosion resistance, and high conductivity. Copper or the like is preferable. Note that the same material may be used for the positive electrode current collector plate and the negative electrode current collector plate, or different materials may be used.
  • ⁇ Use positive terminal lead and negative terminal lead as required.
  • a terminal lead used in a known lithium ion secondary battery can be used.
  • the part taken out from the battery outer packaging material 29 has a heat insulating property so as not to affect the product (for example, automobile parts, particularly electronic devices) by contacting with peripheral devices or wiring and causing leakage. It is preferable to coat with a heat shrinkable tube or the like.
  • ⁇ Battery exterior material> As the battery exterior material 29, a known metal can case can be used, and a bag-like case using a laminate film containing aluminum that can cover the power generation element can be used.
  • a laminate film having a three-layer structure in which PP, aluminum, and nylon are laminated in this order can be used as the laminate film, but the laminate film is not limited thereto.
  • a laminate film is desirable from the viewpoint that it is excellent in high output and cooling performance, and can be suitably used for a battery for large equipment for EV and HEV.
  • said lithium ion secondary battery can be manufactured with a conventionally well-known manufacturing method.
  • FIG. 2 is a perspective view showing the appearance of a stacked flat lithium ion secondary battery.
  • the stacked flat lithium ion secondary battery 50 has a rectangular flat shape, and a positive current collector 58 for taking out power from both sides thereof, a negative current collector, and the like.
  • the electric plate 59 is pulled out.
  • the power generation element 57 is wrapped by the battery outer packaging material 52 of the lithium ion secondary battery 50, and the periphery thereof is heat-sealed.
  • the power generation element 57 pulls out the positive electrode current collector plate 58 and the negative electrode current collector plate 59 to the outside. Sealed.
  • the power generation element 57 corresponds to the power generation element 21 of the lithium ion secondary battery (stacked battery) 10 shown in FIG.
  • the power generation element 57 is formed by laminating a plurality of single battery layers (single cells) 19 including a positive electrode (positive electrode active material layer) 13, an electrolyte layer 17, and a negative electrode (negative electrode active material layer) 15.
  • the lithium ion secondary battery is not limited to a laminated flat shape (laminate cell).
  • a cylindrical shape coin cell
  • a prismatic shape square cell
  • it may be a cylindrical cell, and is not particularly limited.
  • the cylindrical or prismatic shape is not particularly limited, for example, a laminate film or a conventional cylindrical can (metal can) may be used as the exterior material.
  • the power generation element is covered with an aluminum laminate film. With this configuration, weight reduction can be achieved.
  • the removal of the positive electrode current collector plate 58 and the negative electrode current collector plate 59 shown in FIG. 2 is not particularly limited.
  • the positive electrode current collector plate 58 and the negative electrode current collector plate 59 may be drawn out from the same side, or the positive electrode current collector plate 58 and the negative electrode current collector plate 59 may be divided into a plurality of parts and taken out from each side. It is not limited to the one shown in FIG.
  • a terminal instead of the current collector plate, for example, a terminal may be formed using a cylindrical can (metal can).
  • the negative electrode and the lithium ion secondary battery using the negative electrode active material for the lithium ion secondary battery of the present embodiment are large vehicles such as electric vehicles, hybrid electric vehicles, fuel cell vehicles, and hybrid fuel cell vehicles. It can be suitably used as a capacity power source. That is, it can be suitably used for a vehicle driving power source and an auxiliary power source that require high volume energy density and high volume output density.
  • the lithium ion battery is exemplified as the electric device.
  • the present invention is not limited to this, and can be applied to other types of secondary batteries and further to primary batteries. It can also be applied to capacitors as well as batteries.
  • samples 19 to 33 an alloy thin film was formed so that sample 19 was a Si metal, samples 20 to 27 were Si—C binary alloys, and samples 28 to 33 were Si—Al binary alloys. Specifically, only the necessary target among Si, Al, and C targets is used, the sputtering time is fixed, and the power of the DC power source of the target to be used is changed within the above range, so that it can be formed on the Ni substrate. An amorphous Si thin film or a binary alloy thin film was formed.
  • DC power source 2 Si target
  • DC power source 1 C target
  • DC power source 3 Al target
  • the component compositions of these alloy thin films are shown in Table 1 and FIGS.
  • the obtained alloy thin film was analyzed by the following analysis method and analyzer.
  • 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.
  • LiPF 6 a lithium hexafluorophosphate
  • the discharge capacity at the 50th cycle was obtained, and the maintenance ratio relative to the discharge capacity at the first cycle was calculated.
  • the degradation mode of the electrolyte is also included in the cycle characteristics (conversely, the use of a high-performance electrolyte improves the cycle characteristics). It was.
  • the results are also shown in Table 1.
  • the discharge capacity indicates a value calculated per alloy weight. “Discharge capacity (mAh / g)” is per pure Si or alloy weight, and when Li reacts with Si—Al—C alloy (Si—C alloy, pure Si or Si—Al alloy). Indicates capacity.
  • “initial capacity” in this specification corresponds to “discharge capacity (mAh / g)” of the initial cycle (first cycle).
  • discharge capacity maintenance rate (%) at the 50th cycle represents an index of “how much capacity is maintained from the initial capacity”.
  • the calculation formula of the discharge capacity retention rate (%) is as follows.
  • the discharge capacity maintenance rate at the 50th cycle was calculated by the following formula. The results are also shown in Table 1.
  • Charge / discharge efficiency (%) in the table represents an index of “how much Li moves in the charge / discharge process” in the first cycle.
  • the calculation formula of charge / discharge efficiency (%) is as follows.
  • the batteries of Samples 1 to 18, particularly the samples in the composition range surrounded by the thick solid line in FIGS. 7 to 9, have a discharge capacity at the first cycle of the existing carbon-based negative electrode active material (carbon / graphite). It has been found that an extremely high capacity that cannot be realized with a negative electrode material) can be realized. Similarly, it was confirmed that a higher capacity (initial capacity of 1113 mAh / g or more) can be realized as compared with the existing high capacity Sn-based alloy negative electrode active material.
  • the charge / discharge efficiency in the first cycle is as high as 94% or more, preferably 97% or more, as compared with the batteries of samples 19 to 33. It was.
  • the cycle durability which is in a trade-off relationship with the increase in capacity, is also compared with the existing Sn-based negative electrode active material having a high capacity but inferior in cycle durability and the multi-component alloy negative electrode active material described in Patent Document 1.
  • the cycle durability can be remarkably improved. Specifically, it was confirmed that a remarkably excellent cycle durability with a high discharge capacity maintenance rate at the 50th cycle of 64% or more, preferably 74% or more, particularly preferably 81% or more can be realized. Therefore, the batteries of Samples 1 to 18, especially the samples in the composition range surrounded by the thick solid line in FIGS. 7 to 9 have a large discharge capacity maintenance rate compared to the other samples of batteries. It was found that high capacity can be maintained more efficiently by suppressing the decrease in capacity and effective capacity.
  • FIG. 10 shows all charge / discharge curves from 1 to 50 cycles in the charge / discharge test using the battery of sample 7.
  • the ternary alloy of the present embodiment maintains a high cycle characteristic (particularly, a high discharge capacity maintenance rate at the 50th cycle) and has a high balance between the initial capacity and the initial charge / discharge efficiency.
  • the mechanism shown can be inferred as follows.
  • discharge capacity maintenance rate (%) at the 50th cycle or the 100th cycle represents an index of “how much capacity is maintained from the initial capacity”.
  • the calculation formula of the discharge capacity retention rate (%) is as follows.
  • symbol B of FIG. 12 is Si content is more than 47 mass% and less than 95 mass%, Al content is more than 2 mass% and less than 48 mass%, and Nb content is 1 mass.
  • the range of the symbol B corresponds to the range of the reference examples B1 to B11. From Table 2, it can be seen that a lithium ion secondary battery using this alloy is particularly excellent in discharge capacity retention after 50 cycles.
  • the range of C in FIG. 13 is that the Si content is more than 61 mass% and less than 84 mass%, the Al content is more than 2 mass% and less than 25 mass%, and the Nb content is 2 mass.
  • the range of C in FIG. 13 corresponds to Reference Examples B2 to B6.
  • the range of the symbol D in FIG. 13 is that the Si content is more than 47 mass% and less than 56 mass%, the Al content is more than 33 mass% and less than 48 mass%, and the Nb content is 1 mass.
  • An alloy whose content is more than% and less than 16% by mass and the balance is an inevitable impurity.
  • the range of the symbol D in FIG. 13 corresponds to Reference Examples B8 to B11.
  • lithium ion secondary batteries using alloys in the ranges of C and D are particularly excellent in discharge capacity retention after 100 cycles.
  • the Si 50 Al 47 C 3 other than the other alloys used in the present invention Si x Al y C z A a, and among the Si x Al y Nb z A a , other than Si 50 Al 47 C 3 ), The same or similar results as in the following examples using Si 50 Al 47 C 3 are obtained.
  • the other alloys used in the present invention have the same characteristics as Si 50 Al 47 C 3 . That is, when an alloy having the same characteristics is used, the same result can be obtained even if the type of the alloy is changed.
  • Example 1 [Manufacture of Si alloy]
  • the Si alloy was manufactured by a mechanical alloy method (or arc plasma melting method). Specifically, using a planetary ball mill device P-6 manufactured by Fricht, Germany, zirconia pulverized balls and raw material powders of each alloy were charged into a zirconia pulverized pot and alloyed at 600 rpm for 48 hours.
  • Li 1.85 Ni 0.18 Co 0.10 Mn 0.87 O 3 which is a positive electrode active material was produced by the method described in Example 1 (paragraph 0046) of JP2012-185913. Then, 90 parts by mass of this positive electrode active material, 5 parts by mass of acetylene black as a conductive auxiliary agent, and 5 parts by mass of polyvinylidene fluoride as a binder are mixed and dispersed in N-methylpyrrolidone to obtain a positive electrode slurry. It was.
  • the obtained positive electrode slurry was uniformly applied to both surfaces of a positive electrode current collector made of an aluminum foil having a thickness of 20 ⁇ m so that the thickness of the positive electrode active material layer was 30 ⁇ m, and dried to obtain a positive electrode. It was.
  • the positive electrode produced above and the negative electrode were made to face each other, and a separator (polypropylene microporous film, film thickness: 20 ⁇ m) was disposed therebetween.
  • a separator polypropylene microporous film, film thickness: 20 ⁇ m
  • the laminate of the negative electrode, the separator, and the positive electrode was disposed on the bottom side of a coin cell (CR2032, material: stainless steel (SUS316)).
  • a gasket is attached, the following electrolyte is injected with a syringe, a spring and a spacer are stacked, and the upper side of the coin cell is overlapped and sealed by caulking.
  • a lithium ion secondary battery was obtained.
  • lithium (LiPF 6) was used as the concentration was such that 1 mol / L.
  • Example 2 A negative electrode and a battery were produced in the same manner as in Example 1 except that the Si alloy was changed to 4.6 parts by mass and the graphite was changed to 87.4 parts by mass. In addition, the content rate of Si alloy in a negative electrode active material is 5%.
  • Example 3 A negative electrode and a battery were produced in the same manner as in Example 1 except that the Si alloy was changed to 6.44 parts by mass and the graphite was changed to 85.56 parts by mass. In addition, the content rate of Si alloy in a negative electrode active material is 7%.
  • Example 4 A negative electrode and a battery were produced in the same manner as in Example 1 except that the Si alloy was changed to 9.2 parts by mass and the graphite was changed to 82.8 parts by mass. In addition, the content rate of Si alloy in a negative electrode active material is 10%.
  • Example 5 A negative electrode and a battery were produced in the same manner as in Example 1 except that the Si alloy was changed to 11.04 parts by mass and the graphite was changed to 80.96 parts by mass. In addition, the content rate of Si alloy in a negative electrode active material is 12%.
  • Example 6 A negative electrode and a battery were produced in the same manner as in Example 1 except that the Si alloy was changed to 13.8 parts by mass and the graphite was changed to 78.2 parts by mass. In addition, the content rate of Si alloy in a negative electrode active material is 15%.
  • Example 7 A negative electrode and a battery were produced in the same manner as in Example 1 except that the Si alloy was changed to 18.4 parts by mass and the graphite was changed to 73.6 parts by mass. In addition, the content rate of Si alloy in a negative electrode active material is 20%.
  • Example 8 A negative electrode and a battery were produced in the same manner as in Example 1 except that the Si alloy was changed to 23.0 parts by mass and the graphite was changed to 69.0 parts by mass. In addition, the content rate of Si alloy in a negative electrode active material is 25%.
  • Example 9 A negative electrode and a battery were produced in the same manner as in Example 1 except that the Si alloy was changed to 27.6 parts by mass and the graphite was changed to 64.4 parts by mass. In addition, the content rate of Si alloy in a negative electrode active material is 30%.
  • Example 10 A negative electrode and a battery were produced in the same manner as in Example 1 except that the Si alloy was changed to 36.8 parts by mass and the graphite was changed to 55.2 parts by mass. In addition, the content rate of Si alloy in a negative electrode active material is 40%.
  • Example 11 A negative electrode and a battery were produced in the same manner as in Example 1 except that the Si alloy was changed to 46.0 parts by mass and the graphite was changed to 46.0 parts by mass. In addition, the content rate of Si alloy in a negative electrode active material is 50%.
  • Example 12 A negative electrode and a battery were produced in the same manner as in Example 1 except that the Si alloy was changed to 55.2 parts by mass and the graphite was changed to 36.8 parts by mass. In addition, the content rate of Si alloy in a negative electrode active material is 60%.
  • Example 13 A negative electrode and a battery were produced in the same manner as in Example 1 except that the Si alloy was changed to 64.4 parts by mass and the graphite was changed to 27.6 parts by mass. In addition, the content rate of Si alloy in a negative electrode active material is 70%.
  • the batteries using the negative electrode active material obtained by mixing the Si alloy and graphite in Examples 1 to 13 maintain high cycle characteristics and have high initial capacity and good balance. It is understood that it exhibits properties.
  • Lithium ion secondary battery (stacked battery), 11 positive electrode current collector, 12 negative electrode current collector, 13 positive electrode active material layer, 15 negative electrode active material layer, 17 electrolyte layer, 19 cell layer, 21, 57 power generation element, 25, 58 positive current collector, 27, 59 negative electrode current collector plate, 29, 52 Battery exterior material (laminate film).

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Abstract

Le problème décrit par l'invention est de fournir une électrode négative pour un dispositif électrique tel qu'une cellule rechargeable Li-ion, qui maintient des caractéristiques élevées de cycle et a des caractéristiques bien équilibrées, y compris une capacité initiale élevée. La solution de l'invention porte sur une électrode négative pour un dispositif électrique, avec un collecteur et avec une couche électrode comprenant une substance active d'électrode négative, un matériau assistant conducteur, et un liant qui sont agencés sur la surface du collecteur. La substance active d'électrode négative comprend un mélange de : un alliage décrit par la formule (1) (dans la formule (1), M est au moins un métal sélectionné dans un groupe constitué de C, Nb et une combinaison de ceux-ci, A représente des impuretés inévitables, x, y, z et a représentent des valeurs de fractions massiques en %, 0<x<100, 0<y<100, 0<z<100, 0≤a<0,5, et x+y+z+a=100) ; et un matériau à base de carbone.
PCT/JP2013/081158 2012-11-22 2013-11-19 Électrode négative pour dispositif électrique et dispositif électrique l'utilisant WO2014080903A1 (fr)

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2016018654A (ja) * 2014-07-08 2016-02-01 株式会社日立製作所 リチウムイオン二次電池

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JP2004228059A (ja) * 2002-11-29 2004-08-12 Mitsui Mining & Smelting Co Ltd 非水電解液二次電池用負極及びその製造方法並びに非水電解液二次電池
JP2012114043A (ja) * 2010-11-26 2012-06-14 Nissan Motor Co Ltd 電気デバイス用Ｓｉ合金負極活物質
JP2012199213A (ja) * 2011-03-07 2012-10-18 Nissan Motor Co Ltd 電気デバイス用の負極活物質、電気デバイス用の負極及び電気デバイス

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Publication number Priority date Publication date Assignee Title
JP2004228059A (ja) * 2002-11-29 2004-08-12 Mitsui Mining & Smelting Co Ltd 非水電解液二次電池用負極及びその製造方法並びに非水電解液二次電池
JP2012114043A (ja) * 2010-11-26 2012-06-14 Nissan Motor Co Ltd 電気デバイス用Ｓｉ合金負極活物質
JP2012199213A (ja) * 2011-03-07 2012-10-18 Nissan Motor Co Ltd 電気デバイス用の負極活物質、電気デバイス用の負極及び電気デバイス

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Publication number Priority date Publication date Assignee Title
JP2016018654A (ja) * 2014-07-08 2016-02-01 株式会社日立製作所 リチウムイオン二次電池

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