JP2014187005A - Negative electrode active material for power storage - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a negative electrode active material for a power storage excellent in initial charging and discharging efficiency while having high capacity density and excellent cycle characteristics.SOLUTION: The negative electrode active material for a power storage contains SnO of 25 to 75%, PO+SiOof 5 to 55%, LiO+NaO of 4 to 40%, and BOof 0 to 6% at mol% in terms of oxide.

Description

  The present invention relates to a negative electrode active material for power storage devices used for portable electronic devices, electric vehicles, electric tools, backup emergency power supplies, and the like.

  In recent years, with the spread of portable personal computers and mobile phones, there is an increasing demand for higher capacity and smaller size of power storage devices such as lithium ion secondary batteries. If the capacity of the electricity storage device is increased, it will be easy to reduce the size of the battery. Therefore, there is an urgent need to develop the capacity of the electricity storage device.

  Generally, carbon materials such as graphitic carbon materials are used for negative electrode active materials for power storage devices. However, since the graphitic carbon material has a theoretical capacity of about 372 mAh / g, there is a problem that it is difficult to increase the capacity of the battery.

  A negative electrode active material containing Sn has been proposed as a negative electrode active material capable of inserting and extracting Li ions and Na ions and having a higher capacity density than a negative electrode active material made of a carbon material (for example, Non-patent document 1). However, the negative electrode active material containing Sn has a remarkably large volume change due to the occlusion and release reaction of Li ions and Na ions during charge and discharge, so that the structure of the negative electrode active material deteriorates and cracks when repeatedly charged and discharged. Is likely to occur. As cracks progress, in some cases, cavities are formed in the negative electrode active material and may be pulverized. When a crack occurs in the negative electrode active material, the electron conduction path is broken, so that there is a problem in that the discharge capacity (cycle characteristics) after repeated charge and discharge is reduced.

  Therefore, an oxide material containing Sn and P has been proposed as a negative electrode active material having a higher capacity density than a negative electrode active material made of a carbon material and excellent in cycle characteristics (see, for example, Patent Document 1). ).

  In this negative electrode active material, the Sn component becomes a site for inserting and extracting Li ions and Na ions. In addition, the component containing P becomes an oxide matrix component, and the network composed of P and O surrounds the Sn component, thereby mitigating volume changes that occur when the Sn component occludes and releases Li ions and Na ions. And there exists an effect | action which improves charging / discharging cycling characteristics.

JP 2011-187434 A

M.M. Winter, J.A. O. Besenhard, Electrochimica Acta, 45 (1999), p. 31

  In the negative electrode active material made of an oxide material containing Sn and P, at the first charge, Sn ions are reduced to metal Sn, and then Li ions and Na ions are occluded in the metal Sn. At the same time, Li ions and Na ions are coordinated around the oxide containing P, thereby stabilizing the structure of the oxide matrix containing P. The coordinated Li ions and Na ions are not released during the subsequent discharge, and cannot move to the positive electrode active material through the electrolyte. As a result, there is a problem that the initial charge / discharge efficiency (ratio of the discharge capacity to the initial charge capacity) decreases.

  The present invention has been made in view of the current state of the prior art described above, and provides a negative electrode active material for an electricity storage device that has high capacity density and excellent cycle characteristics and is excellent in initial charge / discharge efficiency. Objective.

The negative electrode active material for an electricity storage device of the present invention is in mol% in terms of oxide, SnO 25 to 75%, P ₂ O ₅ + SiO _{2 5 to} 55%, Li ₂ O + Na ₂ O 4 to 40%, B ₂ O _3. It contains 0 to 6%.

  Moreover, it is preferable that the negative electrode active material for electrical storage devices of this invention contains an amorphous phase.

  The negative electrode for an electricity storage device according to the present invention includes the negative electrode active material for an electricity storage device.

  ADVANTAGE OF THE INVENTION According to this invention, it becomes possible to provide the negative electrode active material for electrical storage devices excellent in first time charge / discharge efficiency, while having a high capacity density and the outstanding cycling characteristics.

The negative electrode active material for an electricity storage device of the present invention is in mol% in terms of oxide, SnO 25 to 75%, P ₂ O ₅ + SiO _{2 5 to} 55%, Li ₂ O + Na ₂ O 4 to 40%, B ₂ O _3. It contains 0 to 6%. The reason why each component is limited in this way will be described below. In addition, in description of content of the following components,% display points out mol% unless there is particular notice.

SnO is an active material component serving as a site for inserting and extracting Li ions and Na ions, and its content is 25 to 75%. The content of SnO is preferably 27 to 72%, more preferably 30 to 70%, still more preferably 32 to 68%, and still more preferably 34 to 67%. Particularly preferred is 65%. When there is too little content of SnO, the discharge capacity per unit mass of a negative electrode active material will become small. On the other hand, if the content of SnO is too large, the oxide matrix components are relatively small, so the volume change associated with insertion and extraction of Li ions and Na ions during charge / discharge cannot be alleviated, and cycle characteristics deteriorate. Tend to. In the present invention, the content of SnO is oxidized tin component other than SnO (SnO _2, etc.) also refers to that summed in terms of SnO.

P ₂ O ₅ and SiO ₂ are both oxide matrix components, and have the effect of relaxing the volume change of the Sn component associated with insertion and extraction of Li ions and Na ions during charge and discharge, and improving cycle characteristics. Their total content is 5 to 55%. The total content of P ₂ O ₅ and SiO ₂ is preferably 7 to 52%, more preferably 10 to 50%, further preferably 12 to 47%, and 15 to 45%. It is still more preferable that it is 17 to 40%. If the total content of P ₂ O ₅ and SiO ₂ is too small, the volume change of the Sn component that accompanies occlusion and release of Li ions and Na ions during charge / discharge cannot be alleviated, resulting in structural deterioration. It tends to decrease. On the other hand, if the total content of P ₂ O ₅ and SiO ₂ is too large, the Sn component becomes relatively small, and the discharge capacity per unit mass of the negative electrode active material becomes small.

P ₂ O ₅ is a component that improves the Li ion and Na ion conductivity of the oxide matrix. The content of P ₂ O ₅ is preferably 45% or less, more preferably 42% or less, further preferably 40% or less, still more preferably 38% or less, and 35%. Even more preferably, it is particularly preferably 32%. The lower limit is not particularly limited, but is preferably 5% or more, more preferably 7% or more, further preferably 10% or more, and further preferably 12% or more. % Or more is particularly preferable.

In addition, the content of SiO ₂ is preferably 55% or less, more preferably 53% or less, further preferably 51% or less, still more preferably 50% or less, and 47% or less. Is more preferable, and it is particularly preferable that it is 45% or less. The lower limit is not particularly limited, but is preferably 5% or more, more preferably 7% or more, further preferably 10% or more, and further preferably 12% or more. % Or more is particularly preferable.

Both Li ₂ O and Na ₂ O are components that make it difficult to absorb Li ions and Na ions in the oxide matrix during the initial charge, and improve the Li ion and Na ion conductivity, and the total content thereof Is 4-40%. The total content of Li ₂ O and Na ₂ O is preferably 4.5 to 39%, more preferably 5 to 38%, still more preferably 5.5 to 37%, It is still more preferable that it is -36%, and it is especially preferable that it is 6.5-35%. If the total content of Li ₂ O and Na ₂ O is too small, Li ions and Na ions are easily absorbed in the oxide matrix during the initial charge, and the initial charge / discharge efficiency tends to decrease. On the other hand, if the total content of Li ₂ O and Na ₂ O is too large, a heterogeneous crystal composed of Li ₂ O or Na ₂ O and P ₂ O ₅ or SiO ₂ (for example, Li ₃ PO ₄ , Li ₄ SiO ₄ ) is formed in a large amount, and the cycle characteristics are likely to deteriorate. Li ₂ O and Na ₂ O may each be contained alone.

In addition, when the ion occluded or released through the electrolyte from the positive electrode during charge / discharge in the electricity storage device is Li ion, it is preferable to contain Li ₂ O, and in the case of Na ion, Na ₂ O is added. It is preferable to contain.

B ₂ O ₃ is an oxide matrix component, has the effect of relaxing the volume change of the Sn component associated with the storage and release of Li ions and Na ions during charge and discharge, and improving the cycle characteristics. 0-6%. The content of B ₂ O ₃ is preferably 0 to 5%, particularly preferably 0 to 3%. If the B ₂ O ₃ content is too large, the amount of Li ions are absorbed to the oxide matrix is increased, it tends to decrease the initial charge and discharge efficiency of a lithium ion battery.

The value of SnO / P ₂ O ₅ is a molar ratio of preferably 0.8 to 19, more preferably 1 to 18, and particularly preferably 1.2 to 17. When the value of SnO / P ₂ O ₅ is too small, the initial charge / discharge efficiency tends to decrease. On the other hand, if the value of SnO / P ₂ O ₅ is greater than 19, the change in volume of the Sn component accompanying the insertion and extraction of Li ions and Na ions during charge / discharge cannot be mitigated, resulting in structural deterioration, resulting in decreased cycle characteristics. It becomes easy to do.

Further, various components can be added in addition to the above components within the range not impairing the effects of the present invention. Examples of such components include MnO, CuO, ZnO, MgO, CaO, Al ₂ O _{3 and the} like. The total content of the above components is preferably 0 to 25%, more preferably 0 to 23%, further preferably 0 to 21%, and preferably 0.1 to 20%. Particularly preferred.

  The negative electrode active material for an electricity storage device of the present invention preferably contains an amorphous phase. Here, “contains an amorphous phase” means that a broad diffraction line (amorphous halo) is detected in powder X-ray diffraction measurement described later. By containing an amorphous phase, it is possible to improve the Li ion and Na ion conductivity of the oxide matrix. As the degree of crystallinity is smaller (the proportion of the amorphous phase is larger), the volume change of the Sn component at the time of charge / discharge can be alleviated, so that the cycle characteristics tend to improve. Specifically, the degree of crystallinity is preferably 95% or less, more preferably 80% or less, still more preferably 70% or less, still more preferably 50% or less, and 40% It is even more preferable that the ratio is 20% or less. The negative electrode active material is preferably substantially amorphous. Here, “substantially amorphous” means that the crystallinity is 1% or less, and means that no crystalline diffraction line is detected in the powder X-ray diffraction measurement described later.

  The crystallinity is determined by peak separation into a diffraction line profile of 10 to 60 °, a crystalline diffraction line and an amorphous halo, with 2θ values obtained by powder X-ray diffraction measurement using CuKα rays. . Specifically, the integrated intensity obtained by peak-separating a broad diffraction line (amorphous halo) at 10 to 45 ° from the total scattering curve obtained by subtracting the background from the diffraction line profile is Ia, 10 When the total integrated intensity obtained by peak separation of each crystalline diffraction line detected at ˜60 ° is Ic, the crystallinity Xc can be obtained from the following equation.

    Xc = [Ic / (Ic + Ia)] × 100 (%)

  The shape of the negative electrode active material for an electricity storage device of the present invention is not particularly limited, but is preferably a powder. Due to the powder form, in the electricity storage device produced using this negative electrode active material, the contact area between the negative electrode active material and the electrolyte is increased, and the conductivity of Li ions and Na ions between the active material and the electrolyte is increased. Therefore, it is possible to increase the discharge capacity per unit mass of the negative electrode active material and improve the rapid charge / discharge characteristics.

  When the negative electrode active material for an electricity storage device of the present invention is in a powder form, the average particle size is preferably 0.1 to 20 μm, more preferably 0.2 to 15 μm, and 0.3 to 10 μm. Is more preferable, and it is especially preferable that it is 0.5-5 micrometers. The maximum particle size is preferably 150 μm or less, more preferably 100 μm or less, further preferably 75 μm or less, and particularly preferably 55 μm or less. If the average particle size or the maximum particle size is too large, the volume change of the negative electrode active material associated with insertion and extraction of Li ions and Na ions during charge / discharge cannot be relaxed, and it will be easy to peel off from the current collector, resulting in cycle characteristics. Tends to decrease. On the other hand, if the average particle size is too small, the powder is in a poorly dispersed state when formed into a paste, and it tends to be difficult to produce a uniform electrode.

  Here, the average particle size and the maximum particle size are D50 (50% volume cumulative diameter) and D90 (90% volume cumulative diameter), respectively, as the median diameter of primary particles, and were measured by a laser diffraction particle size distribution analyzer. Value.

The negative electrode active material for an electricity storage device of the present invention is produced, for example, by heating and melting raw material powder to vitrify it. In the oxide material containing Sn, the oxidation state of Sn atoms easily changes depending on the melting conditions. When melted in the atmosphere, unwanted crystals such as SnO ₂ and SnP ₂ O ₇ are formed on the surface of the glass melt or in the glass melt. It is easy to be formed. As a result, the initial charge / discharge efficiency and cycle characteristics of the negative electrode active material are likely to deteriorate. Therefore, by performing melting in a reducing atmosphere or an inert atmosphere, it is possible to suppress an increase in the valence of Sn ions in the oxide material, to suppress formation of unwanted crystals, and to be excellent in initial charge / discharge efficiency and cycle characteristics. It is possible to obtain an electricity storage device.

In order to melt in a reducing atmosphere, it is preferable to supply a reducing gas into the melting tank. The reducing gas, by _volume%, it is preferable to use a mixed gas containing N 2 90 to 99.5% and _{H 2 0.5~10%, N 2 92~99} % and _H 2 1 to 8 It is more preferable to use a mixed gas containing%.

  When melting in an inert atmosphere, it is preferable to supply an inert gas into the melting tank. As the inert gas, it is preferable to use any of nitrogen, argon, and helium.

  The reducing gas or the inert gas may be supplied to the upper atmosphere of the molten glass in the melting tank, may be supplied directly from the bubbling nozzle into the molten glass, or both methods may be performed simultaneously.

Moreover, in the manufacturing method of the said negative electrode active material, it becomes easy to obtain the negative electrode active material with few devitrification foreign materials and excellent uniformity by using composite oxide for starting raw material powder. If the negative electrode active material is used, an electricity storage device having a stable discharge capacity can be easily obtained. Examples of such complex oxides include stannous pyrophosphate (Sn ₂ P ₂ O ₇ ) and trilithium phosphate (Li ₃ PO ₄ ).

  Furthermore, in the method for producing a negative electrode material for an electricity storage device of the present invention, the raw material powder preferably contains a metal powder or a carbon powder. Thereby, Sn atoms in the negative electrode material can be shifted to a reduced state. As a result, the Sn valence in the negative electrode material is reduced, and the initial charge efficiency of the electricity storage device can be improved.

  The metal powder preferably contains at least one selected from Sn, Al, Si, and Ti, and more preferably contains at least one selected from Sn, Al, and Si.

  In order to obtain a powder of a predetermined size in the negative electrode active material for an electricity storage device of the present invention, a general pulverizer or classifier is used. For example, a mortar, a ball mill, a vibrating ball mill, a satellite ball mill, a planetary ball mill, a jet mill, a sieve, a centrifugal separator, an air classification, or the like is used.

  A negative electrode material for an electricity storage device can be obtained by adding a binder or a conductive additive to the negative electrode active material for an electricity storage device of the present invention.

  Examples of the binder include cellulose derivatives such as carboxymethylcellulose, hydroxypropylmethylcellulose, hydroxypropylcellulose, hydroxyethylcellulose, ethylcellulose, hydroxymethylcellulose, and water-soluble polymers such as polyvinyl alcohol; thermosetting polyimide, phenolic resin, epoxy resin, urea Examples thereof include thermosetting resins such as resins, melamine resins, unsaturated polyester resins, and polyurethanes; polyvinylidene fluoride.

  Examples of the conductive assistant include highly conductive carbon black such as acetylene black and ketjen black, carbon powder such as graphite, and carbon fiber.

  The negative electrode material for an electricity storage device can be used as an anode for an electricity storage device by applying it to the surface of a metal foil or the like that serves as a current collector.

  As mentioned above, although the negative electrode active material mainly used for a lithium ion secondary battery or a sodium ion secondary battery was demonstrated, the negative electrode active material of this invention is not limited to this, Other non-aqueous secondary batteries In addition, the present invention can also be applied to a hybrid capacitor in which a negative electrode active material used for a lithium ion secondary battery or a sodium ion secondary battery and a positive electrode material for a non-aqueous electric double layer capacitor are combined.

  A lithium ion capacitor and a sodium ion capacitor, which are hybrid capacitors, are one type of asymmetric capacitors that have different charge / discharge principles for the positive and negative electrodes. The lithium ion capacitor has a structure in which a negative electrode for a lithium ion secondary battery and a positive electrode for an electric double layer capacitor are combined. The sodium ion capacitor has a structure in which a negative electrode for a sodium ion secondary battery and a positive electrode for an electric double layer capacitor are combined. Here, the positive electrode forms an electric double layer on the surface and is charged and discharged by utilizing a physical action (electrostatic action), whereas the negative electrode is a lithium ion secondary battery or a sodium ion secondary battery as described above. Similarly, charging / discharging is performed by a chemical reaction (storage and release) of lithium ions or sodium ions.

  A positive electrode active material made of a carbonaceous powder having a high specific surface area such as activated carbon, polyacene, or mesophase carbon is used for the positive electrode of the lithium ion capacitor and the sodium ion capacitor. On the other hand, the negative electrode active material of the present invention can be used for the negative electrode.

  In addition, after charging / discharging the electrical storage device using the negative electrode active material for electrical storage devices of this invention, the said negative electrode active material for electrical storage devices is lithium oxide, sodium oxide, Sn-Li alloy, Sn-Na alloy, or metal May contain tin.

  Examples of the negative electrode active material for an electricity storage device of the present invention will be described below with reference to examples applied to the use of a nonaqueous secondary battery, but the present invention is not limited to these examples.

(1) Preparation of negative electrode active material Various oxides, phosphate raw materials, carbonate raw materials, metal powder or carbon as raw materials so as to have the compositions of Examples 1 to 13 and Comparative Examples 1 to 7 shown in Tables 1 to 3 A raw material powder was prepared using powder and the like. The raw material powder was put into a quartz crucible and melted at 1250 ° C. for 60 minutes in a nitrogen atmosphere using an electric furnace to be vitrified.

  Next, the molten glass was poured out between a pair of rotating rollers and molded while being rapidly cooled to obtain a film-like glass having a thickness of 0.1 to 2 mm. This film-like glass was pulverized with a ball mill and then passed through a sieve having an opening of 20 μm to obtain a glass powder (negative electrode active material) having an average particle diameter of 3 μm.

  The structure of the obtained glass powder was identified by powder X-ray diffraction measurement. The results are shown in Tables 1-3. The glass powders of Examples 1 to 13 had a crystallinity of 10% or less. In particular, the glass powders of Examples 1 to 6 and 8 to 13 were amorphous, and no crystals were detected. Further, the glass powders of Comparative Examples 1 to 4, 6 and 7 were amorphous, and the glass powder of Comparative Example 5 had a crystallinity of 48%.

(2) Production of negative electrode for lithium ion secondary battery For the obtained glass powder, conductive carbon black (SuperC65, manufactured by Timcal) as a conductive auxiliary agent, polyvinylidene fluoride as a binder, glass powder: conductive auxiliary agent Agent: Binder = Weighed to 80: 5: 15 (mass ratio), dispersed in N-methylpyrrolidone (NMP), and then sufficiently stirred with a rotation / revolution mixer to form a slurry. Next, using a doctor blade with a gap of 75 μm, the obtained slurry was coated on a 20 μm thick copper foil as a negative electrode current collector, vacuum-dried with a dryer at 70 ° C., and then between a pair of rotating rollers. An electrode sheet was obtained by pressing through. This electrode sheet was punched to a diameter of 11 mm with an electrode punching machine and dried under reduced pressure at a temperature of 160 ° C. for 8 hours to obtain a circular negative electrode.

(3) Production of test battery (lithium ion secondary battery) Next, the obtained negative electrode was placed on the lower lid of the coin cell with the copper foil surface facing downward, and dried under reduced pressure at 70 ° C. for 8 hours. A test battery was manufactured by laminating a separator made of a polypropylene porous film having a diameter of 16 mm (Celguard # 2400, manufactured by Hoechst Celanese) and metallic lithium as a counter electrode. As the electrolytic solution, 1M LiPF ₆ solution / EC: DEC = 1: 1 (EC = ethylene carbonate, DEC = diethyl carbonate) was used. The test battery was assembled in an environment with a dew point temperature of −40 ° C. or lower.

(4) Charge / Discharge Test The test battery was charged at 30 ° C. from an open circuit voltage to 0 V with CC (constant current) (lithium ion occlusion in the negative electrode active material) to be charged into a unit mass of the negative electrode active material. The amount of electricity (initial charge capacity) was determined. Next, CC discharge (lithium ion release from the negative electrode active material) was performed from 0 V to 1 V, and the amount of electricity (initial discharge capacity) discharged from the unit mass of the negative electrode active material was determined. The C rate was 0.5C. Note that the discharge capacity retention rate refers to the ratio between the initial discharge capacity and the discharge capacity at the 100th cycle.

As shown in Tables 1 and 2, the initial discharge capacities of Examples 1 to 13 are 430 mAh / g or more, the discharge capacity retention rate is 76% or more, the initial charge / discharge efficiency is 54% or more, a high capacity density and an excellent cycle. In addition to having the characteristics, the initial charge and discharge efficiency was excellent. On the other hand, as shown in Table 3, Comparative Examples 1-4, 6, and 7 had a low initial charge / discharge efficiency of 53% or less because the total content of Li ₂ O and Na ₂ O was small. Further, Comparative Example _2, since the content of B 2 _{O 3} is too large, Comparative Example _3, since the B 2 _{O 3} and the content of SnO is too large, the discharge capacity retention ratio was low, less 68%. In Comparative Example 5, since the content of Li ₂ O is too large, heterogeneous crystals are precipitated, the initial discharge capacity is 389mAh / g, the discharge capacity retention ratio was low, 66%.

(5) Production of negative electrode for sodium ion secondary battery Thermosetting polyimide resin as binder for Examples 1 to 13 and Comparative Examples 1, 2, 4, 6 and 7 shown in Tables 1 to 3 (Dreambond, manufactured by IST), substance name SuperC65 (manufactured by Timcal) as a conductive assistant, weighed so that the glass powder: binder: conductive assistant = 80: 15: 5 (mass ratio), these Was dispersed in N-methylpyrrolidone (NMP), and then sufficiently stirred with a rotation / revolution mixer to form a slurry. Next, using a doctor blade with a gap of 100 μm, the obtained slurry was coated on a 20 μm thick copper foil as a negative electrode current collector, dried under reduced pressure at 70 ° C. in a dryer, and then a pair of rotating rollers An electrode sheet was obtained by pressing in between. The electrode sheet was punched to a diameter of 11 mm with an electrode punching machine and dried at 300 ° C. for 3 hours while reducing the pressure to obtain a circular negative electrode.

(6) Production of test battery (sodium ion secondary battery) Next, the obtained negative electrode was placed on the bottom lid of the coin cell with the copper foil surface facing down, and dried under reduced pressure at 70 ° C. for 8 hours. A test battery was manufactured by laminating a separator made of a polypropylene porous film having a diameter of 16 mm and metallic sodium as a counter electrode. As the electrolytic solution, 1M NaPF ₆ solution / EC: DEC = 1: 1 was used. The test battery was assembled in an environment with a dew point temperature of −70 ° C. or lower.

(7) Charge / Discharge Test The above test battery is charged with CC (constant current) at 30 ° C. from open circuit voltage to 0.01 V (sodium ion occlusion in the negative electrode active material) and charged to the negative electrode active material of unit mass. The amount of electricity (initial charge capacity) was determined. Next, CC discharge (sodium ion release from the negative electrode active material) was performed from 0.01 V to 1 V, and the amount of electricity discharged from the unit mass of the negative electrode active material (initial discharge capacity) was determined. The C rate was 0.1C. Tables 4 to 6 show the results of the charge / discharge characteristics. The discharge capacity retention rate is the ratio of the discharge capacity at the 50th cycle to the initial discharge capacity.

As shown in Tables 4 and 5, the initial discharge capacities of Examples 1 to 13 were 251 mAh / g or more, the discharge capacity retention rate was 52% or more, the initial charge / discharge efficiency was 59% or more, a high capacity density and an excellent cycle. In addition to having the characteristics, the initial charge and discharge efficiency was excellent. On the other hand, as shown in Table 6, Comparative Examples 1, ₂ , 4, 6 and 7 had a low initial charge / discharge efficiency of 56% or less because the total content of Li ₂ O and Na ₂ O was small. .

  The negative electrode active material for power storage devices of the present invention is suitable as a negative electrode active material for power storage devices used for portable electronic devices, electric vehicles, electric tools, backup emergency power supplies, and the like.

Claims (3)

In mole percent on the oxide basis, and characterized in that it contains _{SnO 25~75%, P 2 O 5} + SiO 2 5~55%, Li 2 O + Na 2 O 4~40%, the 2 O 3 0~6% _B A negative electrode active material for an electricity storage device.   The negative electrode active material for an electricity storage device according to claim 1, comprising an amorphous phase. A negative electrode for an electricity storage device, comprising the negative electrode active material for an electricity storage device according to claim 1.