ALL-SOLID-STATE LITHIUM ION SECONDARY BATTERY AND MANUFACTURING METHOD OF ALL-SOLID-STATE LITHIUM ION SECONDARY BATTERY

Abstract

Provided is an all-solid-state lithium ion secondary battery including one or more laminates in which a positive electrode layer, a solid electrolyte layer, and a negative electrode layer are arranged in this order, in which at least one collector layer included in at least one of the positive electrode layer or the negative electrode layer is a layer having a specific metal as a constitutional material or a layer having the specific metal in a coating layer, and the solid electrolyte layer contains an amorphous solid electrolyte which contains a lithium-containing oxide containing Li, B, and O, and water and a lithium salt with a specific molar ratio with respect to the lithium-containing oxide.

Description

BACKGROUND OF THE INVENTION

1. Field of the Invention

The present invention relates to an all-solid-state lithium ion secondary battery and a manufacturing method of an all-solid-state lithium ion secondary battery.

2. Description of the Related Art

In the related art, an organic solvent having high ion conductivity has been used as an electrolyte in a lithium ion secondary battery. However, since the organic solvent is flammable, there is a problem in safety. In addition, since the organic solvent is liquid, it is difficult to make the battery compact, and there is also a problem of limitation on capacity in a case where the battery is large.

On the other hand, an all-solid-state lithium ion secondary battery is one of the next-generation batteries which can solve these problems. FIG. 1 shows a basic configuration of the all-solid-state lithium ion secondary battery. An all-solid-state lithium ion secondary battery 10 includes a negative electrode collector layer 1, a negative electrode active material layer 2, a solid electrolyte layer 3, a positive electrode active material layer 4, and a positive electrode collector layer 5 in this order as viewed from the negative electrode side. The respective layers are in contact with each other to form an adjacent structure. By adopting such a structure, during charging, electrons (e⁻) are supplied to the negative electrode side, and lithium ions (Li⁺) which have moved through the solid electrolyte layer 3 are accumulated in the negative electrode. On the other hand, during discharging, lithium ions (Li⁺) accumulated in the negative electrode are returned to the positive electrode side through the solid electrolyte layer 3, and electrons are supplied to an operation portion 6. In the illustrated example, an electric bulb is employed as a model of the operation portion 6, and is lit by the discharging.

As described above, in the all-solid-state lithium ion secondary battery, in order to obtain desired charging and discharging characteristics, the solid electrolyte layer is required to have excellent lithium ion conductivity.

As a solid electrolyte constituting the solid electrolyte layer, a sulfide-based solid electrolyte or an oxide-based solid electrolyte is mainly used.

Since the sulfide-based solid electrolyte is soft and plastically deformed, particles are bonded only by pressure molding. Therefore, the sulfide-based solid electrolyte has a low interface resistance between particles and excellent ion conductivity. However, the sulfide-based solid electrolyte has a problem in that it reacts with water to generate toxic hydrogen sulfide.

On the other hand, the oxide-based solid electrolyte has an advantage of high safety. However, the oxide-based solid electrolyte is hard and is not easily plastically deformed. In order to improve bonding property between particles of the oxide-based solid electrolyte, a high-temperature sintering treatment is required, which is restricted from the viewpoint of production efficiency of the battery, energy cost, and the like. For example, JP2018-052755A discloses a solid electrolyte formed of a lithium-containing oxide having a specific element composition, and it discloses that the solid electrolyte exhibits high ion conductivity. However, in order to use the lithium-containing oxide described in JP2018-052755A as a solid electrolyte sheet, a high-temperature sintering treatment is required.

As a technique for dealing with the problem, for example, WO2021/193204A discloses a composite body containing a lithium compound having a lithium ion conductivity of 1.0×10⁻⁶ S/cm or more at 25° C., and lithium tetraborate in which a reduced pair distribution function G(r) obtained from an X-ray total scattering measurement exhibits a specific profile. According to the technique disclosed in WO2021/193204A, even though the composite body is composed of a lithium-containing oxide, since lithium tetraborate acts as a bond between lithium compounds by plastic deformation, it is possible to form a lithium ion conductor exhibiting excellent lithium ion conductivity by a pressurization treatment, without performing the high-temperature sintering treatment.

SUMMARY OF THE INVENTION

The above-described composite body disclosed in WO2021/193204A is soft even though it is composed of a lithium-containing oxide, and can ensure the binding between particles without performing a sintering treatment or without blending a binder such as an organic polymer, and has characteristics which have not been achieved by the oxide-based solid electrolyte so far. However, as a result of further studies, the present inventors have found that the lithium ion conductivity is not sufficient at the present stage for practical use as the solid electrolyte layer of the all-solid-state lithium ion secondary battery, and there is room for improvement toward practical use.

An object of the present invention is to provide an all-solid-state lithium ion secondary battery that a lithium-containing oxide is used in a solid electrolyte layer, in which the solid electrolyte layer has excellent bonding property between particles even in a case where a high-temperature sintering treatment is not performed or even in a case where a binder such as an organic polymer is not blended, and the all-solid-state lithium ion secondary battery includes a collector layer formed of a metal, which has higher lithium ion conductivity, is excellent in safety, and is difficult to use under conditions for performing high-temperature sintering.

Another object of the present invention is to provide a manufacturing method of an all-solid-state lithium ion secondary battery that a lithium-containing oxide is used in a solid electrolyte layer, in which the solid electrolyte layer has excellent bonding property between particles even in a case where a high-temperature sintering treatment is not performed or even in a case where a binder such as an organic polymer is not blended, and the all-solid-state lithium ion secondary battery includes a collector layer formed of a metal, which has higher lithium ion conductivity, is excellent in safety, and is difficult to use under conditions for performing high-temperature sintering in an atmosphere containing oxygen gas.

The object of the present invention has been achieved by the following methods.

[1]

An all-solid-state lithium ion secondary battery comprising:

• • at least one or more laminates in which a positive electrode layer, a solid electrolyte layer, and a negative electrode layer are arranged in this order,
  • in which at least one of the positive electrode layer or the negative electrode layer includes a collector layer,
  • at least one collector layer is a layer having, as a constitutional material, a metal melted at 670° C. under normal pressure or a layer having the metal in a coating layer, and
  • the solid electrolyte layer contains an amorphous solid electrolyte which contains a lithium-containing oxide containing Li, B, and O, water, and a lithium salt, and in the amorphous solid electrolyte, a value of a ratio of a content of the lithium salt to a content of the lithium-containing oxide is 0.001 to 1.5 in terms of a molar ratio, and a value of a ratio of a content of the water to the content of the lithium-containing oxide is 1 to 12 in terms of a molar ratio.[2]

The all-solid-state lithium ion secondary battery according to [1],

• • in which the metal melted at 670° C. under normal pressure is Al or an Al alloy.[3]

The all-solid-state lithium ion secondary battery according to [1] or [2],

• • in which the lithium-containing oxide includes Li_2+xB_4+yO_7+z,
  • where −0.3<x<0.3, −0.3<y<0.3, and −0.3<z<0.3.[4]

A manufacturing method of an all-solid-state lithium ion secondary battery including at least one or more of the laminates in which a positive electrode layer, a solid electrolyte layer, and a negative electrode layer are arranged in this order, the manufacturing method comprising:

• • manufacturing the laminate of the positive electrode layer, the solid electrolyte layer, and the negative electrode layer at 300° C. or lower in an atmosphere containing oxygen gas,
  • in which at least one of the positive electrode layer or the negative electrode layer includes a collector layer,
  • at least one collector layer is a layer having Cu as a constitutional material or a layer having Cu in a coating layer, and
  • the solid electrolyte layer contains an amorphous solid electrolyte which contains a lithium-containing oxide containing Li, B, and O, water, and a lithium salt, and in the amorphous solid electrolyte, a value of a ratio of a content of the lithium salt to a content of the lithium-containing oxide is 0.001 to 1.5 in terms of a molar ratio, and a value of a ratio of a content of the water to the content of the lithium-containing oxide is 1 to 12 in terms of a molar ratio.

In the present invention or the specification, in description by indicating a numerical range, in a case where an upper limit value and a lower limit value of the numerical range are described separately, any one of the upper limit value and the lower limit value can be appropriately combined to obtain a specific numerical range. On the other hand, in a case where a numerical range expressed using “to” is described by setting a plurality of numerical ranges, the upper limit value and the lower limit value forming the numerical range are not limited to a specific numerical range before and after “to” in a specific combination, and the upper limit value and the lower limit value of each numerical range can be appropriately combined. In the present invention or the specification, any numerical range expressed using “to” refers to a range including the numerical values before and after the “to” as a lower limit value and an upper limit value, respectively.

The all-solid-state lithium ion secondary battery according to the embodiment of the present invention is an all-solid-state lithium ion secondary battery that a lithium-containing oxide is used in a solid electrolyte layer, in which the solid electrolyte layer has excellent bonding property between particles even in a case where a high-temperature sintering treatment is not performed or even in a case where a binder such as an organic polymer is not blended, and the all-solid-state lithium ion secondary battery includes a collector layer formed of a metal, which has higher lithium ion conductivity, is excellent in safety, and is difficult to use under conditions for performing high-temperature sintering.

In addition, with the manufacturing method of an all-solid-state lithium ion secondary battery according to the aspect of the present invention, it is possible to manufacture an all-solid-state lithium ion secondary battery that a lithium-containing oxide is used in a solid electrolyte layer, in which the solid electrolyte layer has excellent bonding property between particles even in a case where a high-temperature sintering treatment is not performed or even in a case where a binder such as an organic polymer is not blended, and the all-solid-state lithium ion secondary battery includes a collector layer formed of a metal, which has higher lithium ion conductivity, is excellent in safety, and is difficult to use under conditions for performing high-temperature sintering in an atmosphere containing oxygen gas.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a cross-sectional view schematically showing an example of a configuration of an all-solid-state lithium ion secondary battery.

FIG. 2 is a diagram showing an example of an X-ray diffraction pattern for describing X-ray diffraction characteristics of a solid electrolyte (I) used in the present invention.

FIG. 3 is a diagram showing an example of a reduced pair distribution function G(r) obtained from an X-ray total scattering measurement of the solid electrolyte (I) used in the present invention.

FIG. 4 is a diagram showing an example of a spectrum obtained in a case where a solid ⁷Li-NMR measurement of the solid electrolyte (I) used in the present invention is performed at 20° C. or 120° C.

FIG. 5 is a diagram showing an example of a spectrum obtained in a case where a solid ⁷Li-NMR measurement of a lithium tetraborate crystal is performed at 20° C. or 120° C.

FIG. 6 is a diagram showing an example of a spectrum obtained in a case where a solid ⁷Li-NMR measurement of the solid electrolyte (I) used in the present invention is performed at 20° C.

FIG. 7 is a diagram in which a peak shown in FIG. 6 is waveform-separated.

FIG. 8 is a diagram showing an example of a Raman spectrum of the solid electrolyte (I) used in the present invention.

FIG. 9 is a diagram showing a Raman spectrum of a lithium tetraborate crystal.

FIG. 10 is a diagram showing a reduced pair distribution function G(r) obtained by an X-ray total scattering measurement of powdery Li₂B₄O₇ crystals.

FIG. 11 is a diagram showing an X-ray diffraction pattern of powdery Li₂B₄O₇ crystals.

DESCRIPTION OF THE PREFERRED EMBODIMENTS

[All-Solid-State Lithium Ion Secondary Battery]

The all-solid-state lithium ion secondary battery according to the embodiment of the present invention (hereinafter, also referred to as “secondary battery according to the embodiment of the present invention”) is an all-solid-state lithium ion secondary battery including at least one or more laminates in which a positive electrode layer, a solid electrolyte layer, and a negative electrode layer are arranged in this order, in which at least one of the positive electrode layer or the negative electrode layer includes a collector layer, and at least one collector layer is a layer having, as a constitutional material, a metal melted at 670° C. under normal pressure or a layer having the metal in a coating layer. The solid electrolyte layer contains an amorphous solid electrolyte (I) having a specific composition described later.

In the secondary battery according to the embodiment of the present invention, since the solid electrolyte (I) having a specific composition described later has excellent particle bonding property, it is possible to manufacture a secondary battery having a solid electrolyte layer in which particles are bonded by processing molding (non-sintering) without depending on a high-temperature sintering step, which is essential in the manufacture of the secondary battery using an oxide-based solid electrolyte in the related art, and in which a high ion conductivity (10⁻³ S/cm) is exhibited. Therefore, it is possible to provide a secondary battery having a configuration in which a metal melted at 670° C. under normal pressure, which is difficult to use under conditions for the high-temperature sintering, is contained in a collector layer as a constitutional material or in a coating layer of a collector layer.

The configuration of the secondary battery according to the embodiment of the present invention is not particularly limited as long as it has one or more laminates in which a positive electrode layer, a solid electrolyte layer, and a negative electrode layer are arranged in this order, and includes a configuration in which a plurality of layers are laminated such that a solid electrolyte layer is disposed between a positive electrode layer and a negative electrode layer adjacent to each other (a configuration of a small-sized laminated battery). Each constitutional layer (including the collector layer and the like) constituting the secondary battery according to the embodiment of the present invention may have a monolayer structure or a multilayer structure.

Among the configurations of the small-sized laminated battery described above, the present invention can be applied, for example, to the configuration of the solid state battery described in paragraphs to of JP2016-001602A, except for the configuration in which the solid electrolyte layer is the solid electrolyte (I) having a specific composition, at least one of the positive electrode layer or the negative electrode layer includes a collector layer, and at least one collector layer is a layer having, as a constitutional material, a metal melted at 670° C. under normal pressure or a layer having the metal in a coating layer.

Hereinafter, each layer of the secondary battery according to the embodiment of the present invention will be described.

<Solid Electrolyte Layer>

The solid electrolyte layer constituting the secondary battery according to the embodiment of the present invention is a layer formed in a layer shape with the amorphous solid electrolyte having a specific composition or a mixture of the solid electrolyte and other components. The amorphous solid electrolyte having a specific composition contains a lithium-containing oxide containing Li, B, and O (hereinafter, also referred to as “lithium-containing oxide”), water, and a lithium salt.

In the amorphous solid electrolyte having a specific composition, a value of a ratio of a content of the lithium salt to a content of the lithium-containing oxide (lithium salt/lithium-containing oxide) is 0.001 to 1.5 in terms of a molar ratio. In addition, in the amorphous solid electrolyte having a specific composition, a value of a ratio of a content of the water to the content of the lithium-containing oxide (water/lithium-containing oxide) is 1 to 12 in terms of a molar ratio.

Hereinafter, the amorphous solid electrolyte having a specific composition, in which each value of the ratios of the content of the lithium salt and the content of the water with respect to the content of the lithium-containing oxide satisfies the above-described specific molar ratio, will also be referred to as “solid electrolyte (I)”. The solid electrolyte (I) is usually an inorganic solid electrolyte.

The solid electrolyte (I) is in an amorphous state (synonymous with a non-crystalline state), and exhibits an elastic characteristic that is likely to be plastically deformed. As a result, in a constitutional layer containing the solid electrolyte (I), such as the solid electrolyte layer, which is formed by a pressurization treatment or the like, adhesiveness between the solid electrolytes (I) and/or adhesiveness between the solid electrolyte (I) and other components in the constitutional layer are improved, so that an interface resistance can be reduced and more excellent ion conductivity can be obtained. By using the solid electrolyte (I), it is possible to form a constitutional layer such as the solid electrolyte layer, which exhibits excellent lithium ion conductivity by a pressurization treatment or the like without performing a high-temperature sintering treatment, even though the solid electrolyte is an oxide-based solid electrolyte having high safety.

The above-described water contained in the solid electrolyte (I) includes at least bound water. The reason why the solid electrolyte (I) exhibits high lithium ion conductivity is not clear, but it is considered that, in the solid electrolyte (I), a soft hydrated layer is easily formed on a surface of the lithium-containing oxide, and a large amount of lithium derived from the lithium salt is contained in the hydrated layer, and as a result, the ion conductivity is further enhanced.

Here, in the present invention or the specification, the “bound water” means water other than water present as free water or an OH group bonded to the lithium-containing oxide. The solid electrolyte (I) is in a state of solid particles (including a state in which the solid particles are bonded to each other) even in a case of containing the water with the above-described content ratio, and functions as a solid electrolyte of the all-solid-state lithium ion secondary battery. That is, the solid electrolyte (I) contains the bound water which is not removed or is difficult to be removed under normal drying conditions. In a case where the solid electrolyte (I) functions as a solid electrolyte of the all-solid-state lithium ion secondary battery in the state of solid particles (a state in which the solid particles can be handled as a powder), the solid electrolyte (I) may contain free water. That is, in the present invention, the “all-solid-state lithium ion secondary battery” includes a form in which the solid electrolyte contains water as long as the solid electrolyte can be handled as the solid particles (solid powder). In addition, the solid electrolyte (I) used in the present invention, in which the value of the ratio of the content of water to the content of the lithium-containing oxide is 12 or less in terms of a molar ratio, is not in any of a paste state or a gel state, but is in the state of solid particles (solid powder).

In the present invention, the “amorphous” solid electrolyte (I) means that the following X-ray diffraction characteristics are satisfied.

(X-Ray Diffraction Characteristics)

In an X-ray diffraction pattern of the solid electrolyte (I) obtained from an X-ray diffraction measurement using a CuKα ray, none of a first peak in which a peak top is located in a range where a diffraction 2θ is 21.6° to 22.0° and a full-width at half maximum is 0.65° or less, a second peak in which a peak top is located in a range where a diffraction 2θ is 25.4° to 25.8° and a full-width at half maximum is 0.65° or less, a third peak in which a peak top is located in a range where a diffraction 2θ is 33.4° to 33.8° and a full-width at half maximum is 0.65° or less, and a fourth peak in which a peak top is located in a range where a diffraction 2θ is 34.4° to 34.8° and a full-width at half maximum is 0.65° or less are present. Alternatively, in the X-ray diffraction pattern, in a case where at least one peak of the first peak, the second peak, the third peak, or the fourth peak described above (hereinafter, referred to as “peak X) is present, an intensity ratio of the at least one peak in the peak X, which is calculated by the following intensity measuring method, is 5.0 or less.

—Intensity Measuring Method—

An average intensity (Av1) in a range of +0.45° to +0.55° from the diffraction angle 2θ of the peak top of the peak X is calculated and an average intensity (Av2) in a range of −0.55° to −0.45° from the diffraction angle 2θ of the peak top of the peak X is calculated, and an arithmetic mean value of Av1 and Av2 is calculated. A value of a ratio of a peak intensity at the peak top of the peak X to the arithmetic mean value (peak intensity at peak top of peak X/arithmetic mean value) is defined as the intensity ratio.

The X-ray diffraction characteristics will be described in more detail.

In a case where none of the first peak, the second peak, the third peak, and the fourth peak described above are present in the X-ray diffraction pattern of the solid electrolyte (I) obtained from the X-ray diffraction measurement using a CuKα ray, the above-described X-ray diffraction characteristics are satisfied, and the solid electrolyte (I) is in an amorphous state.

In addition, even though the above-described peak X is present in the X-ray diffraction pattern of the solid electrolyte (I) obtained from the X-ray diffraction measurement using a CuKα ray, in a case where the intensity ratio of the at least one peak in the peak X, which is obtained by the above-described intensity measuring method, satisfies 5.0 or less, the above-described X-ray diffraction characteristics are satisfied, and the solid electrolyte (I) is in an amorphous state.

Here, the full-width at half maximum (FWHM) of the peak means a peak width (°) at a point of ½ of the peak intensity at the peak top.

The above-described intensity measuring method will be described in more detail with reference to FIG. 2.

FIG. 2 is a diagram showing an example of the peak X appearing in a diffraction pattern of the solid electrolyte (I) obtained from an X-ray diffraction measurement using a CuKα ray. In the X-ray diffraction pattern shown in FIG. 2, a specific peak in which an intensity of a peak top is represented by an intensity 1 is shown. In the intensity measuring method, as shown in FIG. 2, an average intensity (Av1) in a range of +0.45° to +0.55° from the diffraction angle 2θ of the peak top of the peak X is calculated, and an average intensity (Av2) in a range of −0.55° to −0.45° from the diffraction angle 2θ of the peak top of the peak X is calculated. Next, an arithmetic mean value of Av1 and Av2 is calculated, and a value of a ratio of the intensity 1 to the arithmetic mean value is obtained as the intensity ratio. In a case where the above-described X-ray diffraction characteristics are satisfied, it means that the solid electrolyte (I) does not have a crystal structure, or almost does not have a crystal structure and is in an amorphous state.

That is, the above-described first peak to fourth peak are mainly peaks derived from a crystal structure in the solid electrolyte (for example, a crystal structure of lithium tetraborate), and a case where these peaks are not present means that the solid electrolyte is in an amorphous state. In addition, even though at least one of the first peak to the fourth peak is present, a case where the intensity ratio of the at least one peak in the present peaks X is 5.0 or less means that almost no crystal structure which hinders the effect of the present invention is present in the solid electrolyte (I). For example, a peak derived from a specific component (for example, the lithium salt) may overlap with any one of the above-described first peak to fourth peak. However, in the amorphous solid electrolyte, all of the first peak to the fourth peak are usually decreased. Therefore, even in a case where a peak due to the specific component overlap with any one of the first peak to the fourth peak and one large peak appears, it can be said that the presence of at least one peak X in which the intensity ratio is equal to or less than a predetermined value indicates that the solid electrolyte (I) is in an amorphous state.

The above-described X-ray diffraction measurement is performed using a CuKα ray under measurement conditions of 0.01°/step and 3°/min.

In the X-ray diffraction pattern of the solid electrolyte (I) obtained from the X-ray diffraction measurement using a CuKα ray, it is preferable that none of the first peak, the second peak, the third peak, and the fourth peak described above is present, or even in a case where at least one peak X of the first peak, the second peak, the third peak, and the fourth peak described above is present, the intensity ratio of the at least one peak in the peak X is 3.0 or less.

Among these, it is more preferable that none of the first peak, the second peak, the third peak, and the fourth peak described above is present, or even in a case where at least one peak X of the first peak, the second peak, the third peak, and the fourth peak described above is present, the intensity ratio of the at least one peak in the peak X is 2.0 or less.

In the above-described X-ray diffraction pattern, in a case where two or more peaks in which a peak top is located in a range of 21.6° to 22.0° and the full-width at half maximum is 0.65° or less are present, a peak having the highest diffracted X-ray intensity is selected as the first peak to determine the above-described X-ray diffraction characteristics.

In addition, in the above-described X-ray diffraction pattern, in a case where two or more peaks in which a peak top is located in a range of 25.4° to 25.8° and the full-width at half maximum is 0.65° or less are present, a peak having the highest diffracted X-ray intensity is selected as the second peak to determine the above-described X-ray diffraction characteristics.

In addition, in the above-described X-ray diffraction pattern, in a case where two or more peaks in which a peak top is located in a range of 33.4° to 33.8° and the full-width at half maximum is 0.65° or less are present, a peak having the highest diffracted X-ray intensity is selected as the third peak to determine the above-described X-ray diffraction characteristics.

In addition, in the above-described X-ray diffraction pattern, in a case where two or more peaks in which a peak top is located in a range of 34.4° to 34.8° and the full-width at half maximum is 0.65° or less are present, a peak having the highest diffracted X-ray intensity is selected as the fourth peak to determine the above-described X-ray diffraction characteristics.

(X-Ray Total Scattering Characteristics)

The solid electrolyte (I) preferably satisfies the following requirement A-1 as X-ray total scattering characteristics. In addition, in a case where the solid electrolyte (I) satisfies the above-described X-ray diffraction characteristics, the solid electrolyte (I) generally satisfies the following requirement A-2.

—Requirement A-1—

In a reduced pair distribution function G(r) of the solid electrolyte (I) obtained from an X-ray total scattering measurement, a first peak in which a peak top is located in a range where r is 1.43±0.2 Å and a second peak in which a peak top is located in a range where r is 2.40±0.2 Å are present, G(r) of the peak top of the first peak is more than 1.0, and G(r) of the peak top of the second peak is 0.8 or more.

—Requirement A-2—

In the reduced pair distribution function G(r) of the solid electrolyte (I) obtained from an X-ray total scattering measurement, an absolute value of G(r) in a range where r is more than 5 Å and 10 Å or less is less than 1.0.

In a case where the solid electrolyte (I) satisfies the requirement A-1 and the requirement A-2, the solid electrolyte (I) has a short-range ordered structure related to interatomic distances of B—O and B—B, but has almost no long-range ordered structure. Therefore, the oxide solid electrolyte itself exhibits an elastic characteristic of being softer and more easily plastically deformable than the lithium-containing oxide in the related art. As a result, in a layer containing the solid electrolyte (I) which is formed by a pressurization treatment or the like, adhesiveness between the solid electrolytes (I) and/or adhesiveness between the solid electrolyte (I) and other components in the constitutional layer such as the solid electrolyte layer are improved, and it is presumed that an interface resistance can be reduced and more excellent ion conductivity can be obtained.

The requirement A-1 and the requirement A-2 will be described in more detail with reference to the drawings.

FIG. 3 shows an example of the reduced pair distribution function G(r) of the solid electrolyte (I) obtained by an X-ray total scattering measurement. A vertical axis of FIG. 3 is a reduced pair distribution function obtained by subjecting X-ray scattering to Fourier transform, and it indicates the probability that an atom is present at a position of a distance r. The X-ray total scattering measurement can be performed using SPring-8 BL04B2 (acceleration voltage: 61.4 keV, wavelength: 0.2019 Å). The reduced pair distribution function G(r) is obtained by converting a scattering intensity I_obs which is obtained experimentally according to the following procedure.

First, the scattering intensity I_obs is represented by the following expression (1). In addition, a structure factor S(Q) is obtained by dividing a coherent scattering I_coh by the product of the number N of atoms and the square of an atomic scattering factor f, as represented by the following expression (2).

$\begin{array}{cc}{I}_{\mathrm{obs}}=I_{\mathrm{coh}}+I_{\mathrm{incoh}}+I_{\mathrm{fluorescence}}& \left(1\right)\end{array}$ $\begin{array}{cc}S\left(Q\right)=\frac{I_{\mathrm{coh}}}{{\mathrm{Nf}}^2}& \left(2\right)\end{array}$

The structure factor S(Q) is used for pair distribution function (PDF) analysis. In the above expression (2), a required intensity is solely the coherent scattering I_coh. The incoherent scattering I_incoh and the X-ray fluorescence I_fluorescence can be subtracted from the scattering intensity I_obs by a blank measurement, subtraction using a theoretical expression, and a discriminator of a detector.

The coherent scattering I_coh is represented by Debye's scattering expression (the following expression (3)) (N: total number of atoms, f: atomic scattering factor, r_ij: interatomic distance between i and j).

$\begin{array}{cc}{I}_{\mathrm{coh}}=\sum _{i=1}^N\sum _{j=1}^N{f}_i{f}_j\frac{\sin {\mathrm{Qr}}_{\mathrm{ij}}}{{\mathrm{QR}}_{\mathrm{ij}}}& \left(3\right)\end{array}$

Focusing on any atom, in a case where an atomic density at the distance r is denoted by ρ(r), the number of atoms present inside a sphere having a radius of r to r+d(r) is 4πr²ρ(r)dr, and thus the above expression (3) is represented by the following expression (4).

$\begin{array}{cc}{I}_{\mathrm{coh}}={\mathrm{Nf}}^2\left[1+4\pi {\int }_0^{\infty }{r}^2\rho \left(r\right)\frac{\sin \mathrm{Qr}}{\mathrm{Qr}}\mathrm{dr}\right]& \left(4\right)\end{array}$

In a case where an average density of atoms is denoted by ρ₀, the above expression (4) is modified to obtain the following expression (5).

$\begin{array}{cc}\frac{I_{\mathrm{coh}}}{N}=f^2\left[1+4\pi {\int }_0^{\infty }{r}^2\left(\rho \left(r\right)-{\rho }_0\right)\frac{\sin Qr}{\mathrm{Qr}}\right]& \left(5\right)\end{array}$

From the above expression (5) and the above expression (2), the following expression (6) is obtained.

$\begin{array}{cc}4\pi r^2\rho \left(r\right)=4\pi r^2{\rho }_0+\frac{2r}{\pi }{\int }_0^{\infty }Q\left[S\left(Q\right)-1\right]\sin QrdQ& \left(6\right)\end{array}$

The pair distribution function g(r) is represented by the following expression (7).

$\begin{array}{cc}g\left(r\right)=\frac{{\rho }_r}{{\rho }_0}& \left(7\right)\end{array}$

From the above expression (6) and the above expression (7), the following expression (8) is obtained.

$\begin{array}{cc}g\left(r\right)=1+\frac{1}{2{\pi }^2{\rho }_{0}r}{\int }_0^{\infty }Q\left[S\left(Q\right)-1\right]\sin QrdQ& \left(8\right)\end{array}$

As described above, the pair distribution function can be determined by the Fourier transform of the structural factor S(Q). In order to easily observe medium-range and long-range order, the pair distribution function g(r) is converted into an expression: G(r)=4πr(g(r)−1), which is the reduced pair distribution function G(r) (FIG. 3). The g(r) which oscillates around 0 represents a density difference from the average density at each interatomic distance, and it is larger than the average density of 1 in a case where there is a correlation at a specific interatomic distance. As a result, it reflects the distance and coordination number of elements corresponding to the local to intermediate distance. In a case where the order is lost, ρ(r) approaches the average density, and thus g(r) approaches 1. Therefore, in the amorphous structure, as r is larger, the order is lost, and thus g(r) is 1, that is, G(r) is 0.

In the requirement A-1, as shown in FIG. 3, in the reduced pair distribution function G(r) of the solid electrolyte (I) obtained from an X-ray total scattering measurement, a first peak P1 in which a peak top is located in a range where r is 1.43±0.2 Å and a second peak P2 in which a peak top is located in a range where r is 2.40±0.2 Å are present, G(r) of the peak top of the first peak P1 is more than 1.0 (preferably, 1.2 or more), and G(r) of the peak top of the second peak P2 is 0.8 or more (preferably, more than 1.0).

In FIG. 3, the peak top of the first peak P1 is located at 1.43 Å, and the peak top of the second peak P2 is located at 2.40 Å.

At the position of 1.43 Å, a peak attributed to the interatomic distance of boron (B)-oxygen (O) is present. In addition, at the position of 2.40 Å, a peak attributed to the interatomic distance of boron (B)-boron (B) is present. That is, the fact that the above-described two peaks (the first peak and the second peak) are observed means that periodic structures corresponding to the above-described two interatomic distances are present in the solid electrolyte (I).

In addition, in the requirement A-2, as shown in FIG. 3, the absolute value of G(r) in a range where r is more than 5 Å and 10 Å or less is less than 1.0. As described above, the fact that the absolute value of G(r) in a range where r is more than 5 Å and 10 Å or less is less than 1.0 means that the long-range ordered structure is hardly present in the solid electrolyte (I).

In the above-described reduced pair distribution function G(r), peaks other than the first peak and the second peak may be present in a range where r is 5 Å or less.

A method of forming the solid electrolyte (I) into an amorphous state is not particularly limited. For example, in preparation of the solid electrolyte (I), a method of using, as a raw material, a lithium-containing oxide subjected to a mechanical milling treatment can be adopted. The mechanical milling treatment may be performed in the presence of the lithium salt.

—Mechanical Milling Treatment—

The mechanical milling treatment is a treatment of pulverizing a sample while applying mechanical energy. Examples of the mechanical milling treatment include a milling treatment using a ball mill, a vibration mill, a turbo mill, or a disc mill, and from the viewpoint of obtaining the amorphous solid electrolyte (I) with high productivity, a milling treatment using a ball mill is preferable. Examples of the ball milling include vibration ball milling, rotary ball milling, and planetary ball milling, and planetary ball milling is more preferable.

Conditions of the milling treatment using a ball mill (hereinafter, referred to as a ball milling treatment) are appropriately adjusted depending on the treatment target. A material of pulverization balls (media) is not particularly limited, and examples thereof include agate, silicon nitride, zirconia, alumina, and an iron-based alloy, in which yttria-stabilized zirconia (YSZ) is preferable. An average particle diameter of the pulverization balls is not particularly limited, but from the viewpoint that the solid electrolyte (I) can be produced with high productivity, it is preferably 1 to 10 mm and more preferably 3 to 7 mm. The above-described average particle diameter is obtained by randomly measuring diameters of 50 pulverization balls and arithmetically averaging the measured values. In a case where the pulverization balls are not spherical, a major axis is taken as the diameter. The number of the pulverization balls is not particularly limited.

A material of a pulverization pot in the ball milling treatment is also not particularly limited. Examples thereof include agate, silicon nitride, zirconia, alumina, and an iron-based alloy, and yttria-stabilized zirconia (YSZ) is preferable.

A rotation speed of the ball milling treatment is not particularly limited, and can be set to, for example, 200 to 700 rpm, preferably 350 to 550 rpm. A treatment time of the ball milling treatment is not particularly limited, and can be set to, for example, 10 to 200 hours, preferably 20 to 140 hours. The atmosphere of the ball milling treatment may be an atmosphere of the air or an atmosphere of an inert gas (for example, argon gas, helium gas, nitrogen gas, or the like).

As a method of producing the solid electrolyte (I) using the lithium-containing oxide subjected to the mechanical milling treatment, it is preferable to perform the following steps 1A to 3A.

• • Step 1A: step of subjecting a lithium-containing oxide to a mechanical milling treatment in the presence of a lithium salt
  • Step 2A: step of mixing the product obtained in the step 1A with water
  • Step 3A: step of removing water from the dispersion liquid obtained in the step 2A to obtain the solid electrolyte (I)

In the step 1A, an amount of the lithium salt used is not particularly limited and is appropriately adjusted such that the solid electrolyte (I) defined in the present invention is obtained.

In the above-described step 2A, an amount of water used is not particularly limited. For example, the amount of water used can be set to 10 to 200 parts by mass, preferably 50 to 150 parts by mass with respect to 100 parts by mass of the product obtained in the step 1A.

The method of mixing the product obtained in the step 1A with the water is not particularly limited, and the mixing may be performed in a batchwise manner or may be performed such that the water is added stepwise to the product obtained in the step 1A. In the mixing, an ultrasonic treatment may be performed as necessary. A time of the ultrasonic treatment is not particularly limited, and can be set to, for example, 10 minutes to 5 hours.

The step 3A is a step of removing water from the dispersion liquid obtained in the step 2A to obtain the solid electrolyte (I). The method of removing the water from the dispersion liquid obtained in the step 2A is not particularly limited, and the water may be removed by a heating treatment or may be removed by a vacuum drying treatment.

Drying conditions are not particularly limited, and for example, normal drying conditions that are applied to a general drying treatment can be appropriately applied. Examples thereof include drying conditions applied in Examples. Examples of the normal drying conditions include each of conditions of natural drying (<30% RH), desiccator (<5% RH) drying, and heating drying at 100° C. for 30 minutes to 2 hours.

Before the above-described step 1A, a step 0 of subjecting the lithium-containing oxide to a mechanical milling treatment in an environment in which a lithium salt is not present may be performed.

As the method of producing the solid electrolyte (I), it is also preferable to perform the following steps 1B to 3B, instead of the above-described steps 1A to 3A.

• • Step 1B: step of subjecting a lithium-containing oxide to a mechanical milling treatment
  • Step 2B: step of mixing the product obtained in the step 1B with water and a lithium salt
  • Step 3B: step of removing water from the dispersion liquid obtained in the step 2B to obtain the solid electrolyte (I)

The method of performing the steps 1B to 3B is different from the method of performing the steps 1A to 3A in that the lithium salt is mixed with the lithium-containing oxide which has been subjected to the mechanical milling treatment in the presence of water. Therefore, the difference between the step 1B and the step 1A is that the mechanical milling treatment is performed in the presence of the lithium salt in the step 1A, whereas the mechanical milling treatment is performed without using the lithium salt in the step 1B. Accordingly, in the step 2B, the product obtained in the step 1B is mixed with water and a lithium salt.

A procedure of the step 2B is not particularly limited, and may be a method (method 1) of collectively mixing the product obtained in the step 1B, water, and a lithium salt; a method (method 2) of preparing a dispersion liquid by mixing the product obtained in the step 1B with water, and then mixing the obtained dispersion liquid with a lithium salt; or a method (method 3) of preparing a dispersion liquid 1 by mixing the product obtained in the step 1B with water, preparing a solution 2 by mixing a lithium salt with water, and then mixing the dispersion liquid 1 with the solution 2. In a case where the product obtained in the step 1B is mixed with water, a dispersion treatment such as an ultrasonic treatment may be appropriately performed.

In the method 2, in a case where the dispersion liquid obtained by mixing the product obtained in the step 1B with water is mixed with a lithium salt, the obtained solution is likely to be gelated in a case where the lithium salt is too much, so that the mixing amount of the lithium salt is restricted. On the other hand, in the method 3, even in a case where the product obtained in the step 1B and the lithium salt are mixed in an equimolar amount, the gelation of the solution is less likely to occur, so that the mixing amount of the lithium salt can be increased. From this viewpoint, the method 3 is preferable.

The procedures of the step 3B and the step 3A are the same.

As the method of producing the solid electrolyte (I), it is also preferable to perform the following steps 1C to 3C, instead of the above-described steps 1A to 3A.

• • Step 1C: step of subjecting a lithium-containing oxide to a mechanical milling treatment
  • Step 2C: step of mixing the product obtained in the step 1C with water
  • Step 3C: step of mixing a product obtained by removing water from the dispersion liquid obtained in the step 2C with a lithium salt to obtain the solid electrolyte (I) The procedures of the step 1C and the step 1B are the same.

The procedures of the step 2C and the step 2A are the same.

The step 3C is different from the steps 3A and 3B in that the product obtained by removing water from the dispersion liquid obtained in the step 2C is mixed with a lithium salt.

In the step 3C, an amount of the lithium salt used is not particularly limited and is appropriately adjusted such that the solid electrolyte (I) defined in the present invention is obtained.

The method of mixing the product obtained by removing water from the dispersion liquid obtained in the step 2C with a lithium salt is not particularly limited, and a method of infusing the product with a solution obtained by dissolving the lithium salt in water to mix the two may be adopted.

(Component Composition of Solid Electrolyte (I))

As described above, the solid electrolyte (I) used in the present invention is an amorphous solid electrolyte, and in the solid electrolyte (I), the value of the ratio of the content of the lithium salt to the content of the lithium-containing oxide is 0.001 to 1.5 in terms of a molar ratio, and the value of the ratio of the content of the water to the content of the lithium-containing oxide is 1 to 12 in terms of a molar ratio.

The value of the ratio of the content of the lithium salt to the content of the lithium-containing oxide in the solid electrolyte (I) is preferably 0.001 to 1.2, more preferably 0.01 to 1.2, still more preferably 0.1 to 1.2, and particularly preferably 0.5 to 1.2 in terms of a molar ratio.

In addition, the value of the ratio of the content of the water to the content of the lithium-containing oxide in the solid electrolyte (I) is more preferably 2 to 12 and still more preferably 3 to 11 in terms of molar ratio. In addition, the molar ratio is also preferably 2 to 10, 2 to 8, 2 to 7, or 3 to 7.

The molar amounts of the lithium-containing oxide, the lithium salt, and the water in the solid electrolyte (I) can be determined based on element analysis. Examples of the element analysis include a method of element analysis described in the element composition of the solid electrolyte (I), which will be described later. In addition, the molar amount of the water can also be determined by Karl Fischer method or the like.

The content of the water in the solid electrolyte (I) is preferably 50% by mass or less, more preferably 45% by mass or less, still more preferably 40% by mass or less, and particularly preferably 35% by mass or less. In addition, the content of the water in the solid electrolyte (I) is also preferably 30% by mass or less, or 25% by mass or less.

In addition, the content of the water in the solid electrolyte (I) is usually 5% by mass or more, preferably 10% by mass or more and more preferably 15% by mass or more. Therefore, the content of the water in the solid electrolyte (I) is preferably 5% to 50% by mass, more preferably 5% to 45% by mass, still more preferably 10% to 40% by mass, and particularly preferably 10% to 35% by mass; and also preferably 10% to 30% by mass, 15% to 30% by mass, or 15% to 25% by mass.

The content of the lithium-containing oxide in the solid electrolyte (I) is preferably 20% to 80% by mass, more preferably 20% to 75% by mass, and still more preferably 25% to 70% by mass.

In addition, the content of the lithium salt in the solid electrolyte (I) is preferably 0.5% to 60% by mass, more preferably 1.0% to 55% by mass, and still more preferably 2.0% to 50% by mass; and also preferably 5.0% to 50% by mass.

—Lithium-Containing Oxide—

As described above, the lithium-containing oxide constituting the solid electrolyte (I) contains Li, B, and O.

The above-described lithium-containing oxide is preferably a compound represented by Li_2+xB_4+yO_7+z (−0.3<x<0.3, −0.3<y<0.3, −0.3<z<0.3). That is, in a case where a molar amount of Li is represented by setting a molar amount of B to 4.00, the molar amount of Li is preferably 1.58 to 2.49 (that is, 1.7×4/4.3 to 2.3×4/3.7), and the molar amount of O is preferably 6.23 to 7.89 (that is, 6.7×4/4.3 to 7.3×4/3.7). In other words, assuming that the molar content amount of B is set to 4.00, it is preferable that the relative value of the molar content amount of Li is 1.58 to 2.49 and the molar amount of O is 6.23 to 7.89. Typical examples of such a lithium-containing oxide include lithium tetraborate (Li₂B₄O₇).

In addition, the above-described lithium-containing oxide is also preferably a compound represented by Li_1+xB_3+yO_5+z (−0.3<x<0.3, −0.3<y<0.3, −0.3<z<0.3). Typical examples of such a lithium-containing oxide include lithium triborate (118305).

In addition, the above-described lithium-containing oxide is also preferably a compound represented by Li_3+xB_11+yO_18+z (−0.3<x<0.3, −0.3<y<0.3, −0.3<z<0.3). Typical examples of such a lithium-containing oxide include Li₃B₁₁O₁₈.

In addition, the above-described lithium-containing oxide is also preferably a compound represented by Li_3+xB_7+yO_12+z (−0.3<x<0.3, −0.3<y<0.3, −0.3<z<0.3). Typical examples of such a lithium-containing oxide include Li₃B₇O₁₂.

Therefore, the above-described lithium-containing oxide is preferably at least one of Li_2+xB_4+yO_7+z, Li_1+xB_3+yO_5+z, Li_3+xB_11+yO_18+z, or Li_3+xB_7+yO_12+z described above.

In addition, at least one of LiBO₅, Li₂B₇O₁₂, LiB₂O₃(OH)H₂O, or Li₄B₈O₁₃(OH)₂(H₂O)₃ can also be used as the lithium-containing oxide, instead of the above-described lithium-containing oxide or together with the above-described lithium-containing oxide.

In the solid electrolyte (I), it is preferable that the lithium-containing oxide is in an amorphous state. That is, it is preferable that the lithium-containing oxide in the solid electrolyte (I) is also in a desired amorphous state such that the solid electrolyte (I) is in the above-described amorphous state.

Among these, the lithium-containing oxide is preferably amorphous lithium tetraborate.

—Lithium Salt—

The lithium salt constituting the solid electrolyte (I) used in the present invention is not particularly limited; examples thereof include a salt composed of Li⁺ and an anion; and a salt composed of Li⁺ and an organic anion is preferable and a salt composed of Li⁺ and an organic anion having a halogen atom is more preferable.

It is preferable that the lithium salt constituting the solid electrolyte (I) used in the present invention contains two or more specific elements selected from the group consisting of an element of Group 3 of the periodic table, an element of Group 4 of the periodic table, an element of Group 13 of the periodic table, an element of Group 14 of the periodic table, an element of Group 15 of the periodic table, an element of Group 16 of the periodic table, an element of Group 17 of the periodic table, and H.

As the lithium salt constituting the solid electrolyte (I) used in the present invention, for example, a compound represented by Formula (1) is preferable.

LiN(R_f1SO₂)(R_f2SO₂)  Formula (1)

R_f1 and R_f2 each independently represent a halogen atom or a perfluoroalkyl group. R_f1 and R_f2 may be the same or different from each other.

In a case where R_f1 and R_f2 are a perfluoroalkyl group, the number of carbon atoms in the perfluoroalkyl group is not particularly limited.

R_f1 and R_f2 are preferably a halogen atom or a perfluoroalkyl group having 1 to 6 carbon atoms, more preferably a halogen atom or a perfluoroalkyl group having 1 or 2 carbon atoms, and still more preferably a halogen atom. As the volume of the terminal group increases, the steric hindrance increases, which is a factor that hinders ion conduction. Therefore, in a case where R_f1 and R_f2 are a perfluoroalkyl group, the perfluoroalkyl group preferably has a small number of carbon atoms.

The lithium salt which can be contained in the solid electrolyte (I) used in the present invention is not limited to the above-described compound represented by Formula (1). Examples of the lithium salt which can be contained in the solid electrolyte (I) used in the present invention are shown below.

• • (L-1) Inorganic lithium salt: inorganic fluoride salt such as LiPF₆, LiBF₄, LiAsF₆, and LiSbF₆; perhalogenate such as LiClO₄, LiBrO₄, and LiIO₄; and an inorganic chloride salt such as LiAlCl₄
  • (L-2) Fluorine-containing organic lithium salt: perfluoroalkane sulfonate such as LiCF₃SO₃; fluorosulfonylimide salt or perfluoroalkanesulfonylimide salt such as LiN(CF₃SO₂)₂, LiN(CF₃CF₂SO₂)₂, LiN(FSO₂)₂ (in the present specification, also described as Li(FSO₂)₂N), and LiN(CF₃SO₂)(C₄F₉SO₂); perfluoroalkane sulfonylmethide salt such as LiC(CF₃SO₂)₃; and fluoroalkyl fluorophosphate (preferably, perfluoroalkyl fluorophosphate) such as Li[PF₅(CF₂CF₂CF₃)], Li[PF₄(CF₂CF₂CF₃)₂], Li[PF₃(CF₂CF₂CF₃)₃], Li[PF₅(CF₂CF₂CF₂CF₃)], Li[PF₄(CF₂CF₂CF₂CF₃)₂], and Li[PF₃(CF₂CF₂CF₂CF₃)₃]
  • (L-3) Oxalatoborate salt: lithium bis(oxalato) borate and lithium difluorooxalatoborate

In addition to the above, examples of the lithium salt include LiF, LiCl, LiBr, LiI, Li₂SO₄, LiNO₃, Li₂CO₃, CH₃COOLi, LiAsF₆, LiSbF₆, LiAlCl₄, and LiB(C₆H₅)₄.

Among these, LiPF₆, LiBF₄, LiAsF₆, LiSbF₆, LiClO₄, Li(R_f11SO₂), LiN(R_f11SO₂)₂, LiN(FSO₂)₂, or LiN(R_f11SO₂)(R_f12SO₂) is preferable; and LiPF₆, LiBF₄, LiN(R_f11SO₂)₂, LiN(FSO₂)₂, or LiN(R_f11SO₂)(R_f12SO₂) is more preferable. In these examples, R_f11 and R_f12 each independently represent a perfluoroalkyl group, and the number of carbon atoms therein is preferably 1 to 6, more preferably 1 to 4, and still more preferably 1 or 2. R_f11 and R_f12 may be the same or different from each other. In addition, LiNO₃ or 1,1,2,2,3,3-hexafluoropropane-1,3-disulfonimide lithium is also preferable as the lithium salt.

(Element Composition of Solid Electrolyte (I))

Regarding the solid electrolyte (I), the component composition thereof is described with reference to the compound constituting the solid electrolyte (I). Next, the solid electrolyte (I) will be described from the viewpoint of a preferred element composition. That is, in one aspect of the secondary battery according to the embodiment of the present invention, the solid electrolyte (I) can be specified as follows, for example, based on the element composition without including the “lithium-containing oxide” and the “lithium salt” as the invention specific matters.

In the solid electrolyte (I) used in the present invention, in a case where the molar amount of B in the solid electrolyte (I) is set to 4.00, the molar amount of Li is preferably 1.58 to 3.49 (preferably 1.58 to 3.00, more preferably 1.90 to 3.00, and still more preferably 2.00 to 3.00). In addition, in a case where the molar amount of B in the solid electrolyte (I) is set to 4.00, the molar amount of O is preferably 6.23 to 25.00 (preferably 6.50 to 23.00, more preferably 8.00 to 23.00, still more preferably 10.00 to 23.00, and particularly preferably 10.00 to 18.00). In addition, in a case where the molar amount of B in the solid electrolyte (I) is set to 4.00, it is preferable that molar amounts of elements other than B, Li, and O are each preferably 0.001 to 10.00 (preferably 0.001 to 6.00 and more preferably 0.01 to 5.00).

The content of each element is specified by a general element analysis. As a method of the element analysis, for example, Li and B are analyzed by inductively coupled plasma optical emission spectrometry (ICP-OES); N and the like are analyzed by an inert gas melting method; and F and S are analyzed by combustion ion chromatography. Regarding O, analyzed masses of elements other than O are added together, and the content of O can be calculated as a difference between the analyzed masses and the total amount of the powder. The method of calculating the content of each element is not limited to those described above, and from an analysis result of a content of one kind of element, a content of another element may be estimated in consideration of the structure of the compound to be used.

From the content of each element calculated by the element analysis, the molar amounts of Li, O, and other elements in a case where the molar amount of B is set to 4.00 are calculated.

In a preferred aspect of the solid electrolyte (I), in addition to Li, B, and O, the solid electrolyte (I) further contains one or more elements (E) selected from an element of Group 4 of the periodic table, an element of Group 15 of the periodic table, an element of Group 16 of the periodic table, an element of Group 17 of the periodic table, Si, C, Sc, and Y; and it is more preferable to contain two or more kinds thereof.

Examples of the element of Group 4 of the periodic table include Ti, Zr, Hf, and Rf. Examples of the element of Group 15 of the periodic table include N, P, As, Sb, Bi, and Mc. Examples of the element of Group 16 of the periodic table S, Se, Te, Po, and Lv. Examples of the element of Group 17 of the periodic table include F, Cl, Br, I, At, and Ts.

Among these, it is preferable to contain one or more elements (E) selected from F, Cl, Br, I, S, P, Si, Se, Te, C, Sb, As, Sc, Y, Zr, Ti, Hf, and N; and it is more preferable to contain two or more kinds thereof.

The kind of the element (E) contained in the solid electrolyte (I) may be 3 or more, and is preferably 2 to 5 and more preferably 2 to 4.

As a suitable aspect of the solid electrolyte (I), it is preferable to contain two or more elements (E) selected from F, S, N, P, and C; it is more preferable to contain two or more elements (E) selected from F, S, C, and N; and it is still more preferable to contain three elements (E) of F, S, and N.

In the solid electrolyte (I) containing one or more kinds (preferably two or more kinds) of the above-described elements (E), in a case where the molar amount of Li is represented by setting the molar amount of B in the solid electrolyte (I) to 4.00, the molar amount of Li is preferably 1.58 to 3.49. That is, in a case where the molar content amount of B is set to 4.00, the relative value of the molar content amount of Li is preferably 1.58 to 3.49. Among these, in a case where the molar amount of Li is represented by setting the molar amount of B in the solid electrolyte (I) to 4.00, the molar amount of Li is preferably 1.58 to 3.00, more preferably 1.90 to 3.00, and still more preferably 2.00 to 3.00.

In the solid electrolyte (I) containing one or more kinds (preferably two or more kinds) of the above-described elements (E), in a case where the molar amount of O is represented by setting the molar amount of B in the solid electrolyte (I) to 4.00, the molar amount of O is preferably 6.23 to 25.00. That is, in a case where the molar content amount of B is set to 4.00, the relative value of the molar content amount of O is preferably 6.23 to 25.00. Among these, in a case where the molar amount of O is represented by setting the molar amount of B in the solid electrolyte (I) to 4.00, the molar amount of O is preferably 6.50 to 23.00, more preferably 8.00 to 23.00, still more preferably 10.00 to 23.00, and particularly preferably 10.00 to 18.00.

In the solid electrolyte (I) containing one or more kinds (preferably two or more kinds) of the above-described elements (E), in a case where the molar amount of the elements (E) is represented by setting the molar amount of B in the solid electrolyte (I) to 4.00, each molar amount of the elements (E) is preferably 0.001 to 10.00. That is, in a case where the molar content amount of B is set to 4.00, the relative value of each molar content amount of the elements (E) is preferably 0.001 to 10.00. Among these, in a case where the molar amount of the element (E) is represented by setting the molar amount of B in the solid electrolyte (I) to 4.00, each molar amount of the elements (E) is preferably 0.001 to 6.00 and more preferably 0.01 to 5.00.

Examples of one suitable aspect of the element composition of the solid electrolyte (I) containing one or more kinds (preferably two or more kinds) of the above-described elements (E) include a solid electrolyte containing Li, B, O, F, S, and N, in which, in a case where the molar amount B is set to 4.00, the molar amount of Li is 1.58 to 3.49 (preferably 1.58 to 3.00, more preferably 1.90 to 3.00, and still more preferably 2.00 to 3.00), the molar amount of O is 6.23 to 25.00 (preferably 6.50 to 23.00, more preferably 8.00 to 23.00, still more preferably 10.00 to 23.00, and particularly preferably 10.00 to 18.00), the molar amount of F is 0.001 to 10.00 (preferably 0.01 to 10.00), the molar amount of S is 0.001 to 2.00 (preferably 0.01 to 2.00), and the molar amount of N is 0.001 to 1.00 (preferably 0.005 to 1.00).

The solid electrolyte (I) used in the present invention is in the above-described amorphous state, and as a result, it is preferable that the solid electrolyte (I) exhibits the following characteristics in addition to the above-described X-ray diffraction characteristics.

(Solid ⁷Li-NMR Spectral Characteristics)

In the solid electrolyte (I), a proportion of a full-width at half maximum, which is calculated by the following method from a spectrum obtained by performing a solid ⁷Li-NMR measurement at 20° C. and 120° C., is preferably 50% or less, more preferably 40% or less, and still more preferably 35% or less. The lower limit thereof is not particularly limited, but is usually 10% or more.

The above-described proportion of the full-width at half maximum is obtained by performing a solid ⁷Li-NMR measurement of the solid electrolyte (I) at each of 20° C. and 120° C.; determining a full-width at half maximum (full-width 1 at half maximum) of a peak in which a chemical shift appears in a range of −100 to +100 ppm in a spectrum obtained by a measurement at 20° C., and a full-width at half maximum (full-width 2 at half maximum) of a peak in which a chemical shift appears in a range of −100 to +100 ppm in a spectrum obtained by a measurement at 120° C.; and then calculating a percentage of a proportion of the full-width 2 at half maximum to the full-width 1 at half maximum {(Full-width 2 at half maximum/Full-width 1 at half maximum)×100(%)}. The full-width at half maximum (FWHM) of the peak means a width (ppm) at a point (H/2) of ½ of a height (H) of the peak.

Hereinafter, the above-described characteristic will be described with reference to FIG. 4. FIG. 4 shows an example of the spectrum obtained in a case where the solid ⁷Li-NMR measurement of the solid electrolyte (I) is performed at 20° C. or 120° C. The spectrum shown on the lower side by the solid line in FIG. 4 is a spectrum obtained in a case where the solid ⁷Li-NMR measurement is performed at 20° C.; and the spectrum shown on the upper side by the broken line in FIG. 4 is a spectrum obtained in a case where the solid ⁷Li-NMR measurement is performed at 120° C.

Generally, in the solid ⁷Li-NMR measurement, in a case where mobility of Li⁺ is high, the peak to be obtained is a sharper peak. In the aspect shown in FIG. 4, in a case where the spectrum at 20° C. and the spectrum at 120° C. are compared, the spectrum at 120° C. is sharper. That is, in the aspect shown in FIG. 4, it is indicated that the mobility of Li⁺ is high due to the presence of Li defects. It is conceived that such a solid electrolyte (I) is likely to be plastically deformed due to the above-described defect structure, and thus has excellent hopping property of Li⁺.

For reference, in a case where a general lithium tetraborate crystal is subjected to the solid ⁷Li-NMR measurement at 20° C. or 120° C., the spectrum measured at 20° C. shown by the solid line, shown on the lower side of FIG. 5, and the spectrum measured at 120° C. shown by the broken line, shown on the upper side of FIG. 5, tends to have substantially the same shape. That is, the lithium tetraborate crystal has no Li defects and the like, and as a result, it has a high clastic modulus and is hardly plastically deformed.

Conditions for the above-described solid ⁷Li-NMR measurement are as follows.

The measurement is performed by a single pulse method using a 4 mm HX CP-MAS probe, 90° pulse width: 3.2 μs, observation frequency: 155.546 MHz, observation width: 1397.6 ppm, repetition time: 15 sec, integration: 1 time, and MAS rotation speed: 0 Hz.

In addition, in the solid electrolyte (I) used in the present invention, in a case where a first peak appearing in a range of −100 to +100 ppm in the spectrum obtained in a case where the solid ⁷Li-NMR measurement is performed at 20° C. is waveform-separated, it is preferable that a second peak having a full-width at half maximum of 5 ppm or less appears in a range with a chemical shift of −3 to +3 ppm, and a proportion of an area intensity of the second peak to an area intensity of the first peak is 0.5% or more. The above-described proportion of the area intensity is more preferably 2% or more, still more preferably 5% or more, particularly preferably 10% or more, and most preferably 15% or more. In the aspect of the present invention in which the solid electrolyte (I) contains water, the solid ⁷Li-NMR spectral characteristics of the solid electrolyte (I) tend to be as described above. The upper limit of the above-described proportion of the area intensity is not particularly limited, but is usually 50% or less.

Hereinafter, the above-described characteristic will be described with reference to FIGS. 6 and 7.

FIG. 6 shows an example of the spectrum obtained in a case where the solid ⁷Li-NMR measurement of the solid electrolyte (I) is performed at 20° C. As shown in FIG. 6, in the solid electrolyte (I), a peak (corresponding to the first peak) is observed in a range of −100 to +100 ppm, and a small peak is observed in the vicinity of a chemical shift of 0 ppm, as shown by the broken line at the first peak. As described above, it is considered to be affected the fact that a sharp peak is observed in a case where the mobility of Li⁺ is high.

Next, FIG. 7 shows a diagram in a case where the first peak is waveform-separated. As shown in FIG. 7, the first peak is waveform-separated into a small peak (corresponding to the second peak) represented by the solid line, and a large peak represented by the broken line. The above-described second peak is a peak which appears in a range with a chemical shift of −3 to +3 ppm, and has a full-width at half maximum of 5 ppm or less.

In the solid electrolyte (I), it is preferable that the proportion of the area intensity of the second peak shown by the solid line in FIG. 7 to the area intensity of the first peak (peak before the waveform separation) shown in FIG. 6 {(Area intensity of second peak/Area intensity of first peak)×100(%)} is within the above-described range.

Examples of the method of waveform separation include a method using a known software, and examples of the software include Igor Pro, which is graph processing software manufactured by WaveMetrics, Inc.

(Raman Spectral Characteristics)

In the solid electrolyte (I), a coefficient of determination, which is obtained by performing linear regression analysis according to a least-squares method in a wave number range of 600 to 850 cm⁻¹ in a Raman spectrum of the solid electrolyte (I), is preferably 0.9400 or more and more preferably 0.9600 or more, and also preferably 0.9800 or more. The upper limit thereof is not particularly limited, but is usually 1.0000 or less.

The above-described Raman spectral characteristics will be described with reference to FIG. 8.

First, a Raman spectrum of the solid electrolyte (I) is acquired. Raman imaging is performed as the measuring method of the Raman spectrum. The Raman imaging is a microscopic spectroscopy method which combines Raman spectroscopy with a microscopic technique. Specifically, the Raman imaging is a method of scanning a sample with excitation light to detect measurement light including Raman scattered light, and then visualizing distribution or the like of components based on the intensity of the measurement light.

The measurement conditions for the Raman imaging are as follows: an environment of atmospheric air of 27° C., an excitation light of 532 nm, an objective lens of 100 magnifications, a point scanning according to the mapping method, a step of 1 μm, an exposure time per point of 1 second, the number of times of integration of 1, and a measurement range of a range of 70 μm×50 μm. However, the measurement range may be narrower depending on a film thickness of the sample.

In addition, the Raman spectrum data is subjected to a principal component analysis (PCA) processing to remove noise. Specifically, in the principal component analysis processing, the spectrum is recombined using components having an autocorrelation coefficient of 0.6 or more.

FIG. 8 shows an example of the Raman spectrum of the solid electrolyte (I). In the graph shown in FIG. 8, the vertical axis indicates the Raman intensity, and the lateral axis indicates the Raman shift. A coefficient of determination (coefficient of determination R²) obtained by performing linear regression analysis according to a least-squares method is calculated in a wave number range of 600 to 850 cm⁻¹ of the Raman spectrum shown in FIG. 8. That is, in a wave number range of 600 to 850 cm⁻¹ in the Raman spectrum of FIG. 8, a regression line (the thick broken line in FIG. 8) is determined according to the least-squares method, and the coefficient of determination R² of the regression line is calculated. As the coefficient of determination, a value between 0 (no linear correlation) and 1 (complete linear correlation of the measured values) is taken according to the linear correlation of the measured values.

In the solid electrolyte (I), a peak is not substantially observed in the wave number range of 600 to 850 cm⁻¹ as shown in FIG. 8, and as a result, a high coefficient of determination is exhibited.

The above-described coefficient of determination R² corresponds to the square of the correlation coefficient (Pearson's product-moment correlation coefficient). More specifically, in the present specification, the coefficient of determination R² is calculated according to the following expression. In the expression, x₁ and y₁ represent a wave number in the Raman spectrum and a Raman intensity corresponding to the wave number; x₂ represents the (arithmetic) average of the wave numbers; and y₂ represents the (arithmetic) average of the Raman intensities.

$R^2=\frac{{\left(\sum \left(x_1-x_2\right)·\left(y_1-y_2\right)\right)}^2}{\sum {\left(x_1-x_2\right)}^2·\sum {\left(y_1-y_2\right)}^2}$

On the other hand, for reference, FIG. 9 shows a Raman spectrum of a general lithium tetraborate crystal. As shown in FIG. 9, in a case of a general lithium tetraborate crystal, peaks are observed in a wave number range of 716 to 726 cm⁻¹ and a wave number range of 771 to 785 cm⁻¹, derived from the structure thereof. With the peaks, the coefficient of determination thereof is less than 0.9400 in a case where the coefficient of determination is calculated by performing linear regression analysis according to a least-squares method in a wave number range of 600 to 850 cm⁻¹.

That is, the fact that the coefficient of determination is 0.9400 or more means that the solid electrolyte (I) does not substantially include a crystal structure. Therefore, as a result, it is considered that the solid electrolyte (I) has a characteristic of easily undergoing plastic deformation and a characteristic of excellent hopping property of Lit.

(Infrared Absorption Spectral Characteristics)

In an infrared absorption spectrum of the solid electrolyte (I), a value of a ratio of a maximum absorption intensity in a wave number range of 3,000 to 3,500 cm⁻¹ to a maximum absorption intensity in a wave number range of 800 to 1,600 cm⁻¹ (Maximum absorption intensity in wave number range of 3000 to 3500 cm⁻¹/Maximum absorption intensity in wave number range of 800 to 1600 cm⁻¹) is preferably ⅕ or more (0.2 or more). Among these, the above-described ratio is preferably 3/10 or more and more preferably ⅖ or more. The upper limit thereof is not particularly limited, but is preferably 1 or less.

In the infrared absorption spectrum, an O—H stretching vibration mode is observed in a wave number range of 3,000 to 3,500 cm⁻¹, and a B—O stretching vibration mode is observed in a wave number range of 800 to 1,600 cm⁻¹. In the solid electrolyte (I), a strong absorption intensity derived from the O—H stretching vibration mode is observed, and it is confirmed that a large number of OH groups and/or a large amount of water are contained. In such a solid electrolyte (I), lithium ions tend to move easily, and as a result, the ion conductivity tends to be improved.

In the wave number range of 800 to 1,600 cm⁻¹, a vibration mode derived from the lithium salt can also be observed.

Measurement conditions for the above-described infrared absorption spectrum can be as follows.

The measurement is performed using objective lens: Cassegrain type (NA: 0.65) of 32 magnifications, detector: MCT-A, measurement range: 650 to 4,000 cm⁻¹, resolution: 4 cm⁻¹, and sample cell: diamond cell.

The obtained infrared absorption spectrum is subjected to correction for removing signals derived from water and CO₂ in the air, and the background is further subjected to offset-correction to set the absorption intensity to 0. In addition, the measurement is performed in the air after vacuum drying at 40° C. for 2 hours.

The ion conductivity (27° C.) of the solid electrolyte (I) is not particularly limited, and from the viewpoint of application to various applications, it is preferably 1.0×10⁻⁵ S/cm or more, more preferably 1.0×10⁻⁴ S/cm or more, still more preferably 1.0×10⁻³ S/cm or more, and particularly preferably 3.0×10⁻³ S/cm or more. The upper limit thereof is not particularly limited, but is usually 1.0×10⁻² S/cm or less.

In addition, it is also preferable that the solid electrolyte (I) exhibits the following characteristics or physical properties.

(Mass Reduction Rate)

A mass reduction rate in a case where the solid electrolyte (I) is heated to 800° C. is preferably 20% to 40% by mass and more preferably 25% to 35% by mass. It is considered that the mass reduction by the above-described heating is due to removal of moisture contained in the solid electrolyte (I). In a case where the solid electrolyte (I) contains such moisture, the conductivity of lithium ions can be further improved.

In the above-described heating treatment, the heating is performed at a temperature rising rate of 20° C./sec in a range of 25° C. to 800° C. A known thermogravimetric differential thermal analysis (TG-DTA) device can be used for measuring the mass reduction rate. The above-described mass reduction rate is calculated by {(Mass at 25° C.−Mass at 800° C.)/Mass at 25° C.}×100.

In the measurement of the mass reduction rate, the solid electrolyte (I) is subjected to vacuum drying at 40° C. for 2 hours in advance. In addition, the measurement of the mass reduction rate is performed in the air.

The solid electrolyte layer constituting the secondary battery according to the embodiment of the present invention may contain other components in addition to the solid electrolyte (I).

For example, the solid electrolyte layer can contain a binder consisting of an organic polymer. The organic polymer constituting the binder may be in a particle shape or may be in a non-particle shape. By containing the binder, it is possible to more reliably prevent the solid electrolyte layer or the electrode layer from cracking or the like.

In addition, the solid electrolyte layer may contain a solid electrolyte other than the solid electrolyte (I). The other solid electrolyte means a solid electrolyte in which lithium ions can be moved therein. The solid electrolyte is preferably an inorganic solid electrolyte. Examples of the other solid electrolytes include an oxide-based solid electrolyte, a halide-based solid electrolyte, and a hydride-based solid electrolyte; and an oxide-based solid electrolyte is preferable.

A thickness of the solid electrolyte layer constituting the secondary battery according to the embodiment of the present invention is not particularly limited, and can be set to, for example, 10 to 1,000 μm, preferably 50 to 400 μm. In addition, for example, the thickness thereof can be set to 0.1 to 50 μm, and in this case, it is preferably 1 to 20 μm.

<Positive Electrode Layer>

The positive electrode layer generally includes a positive electrode collector layer and a positive electrode active material layer, but may be composed of the positive electrode active material layer, not including the positive electrode collector layer. In other words, in a case where the positive electrode active material layer also functions as the positive electrode collector layer, it is not necessary to be composed of two layers of the positive electrode active material layer and the positive electrode collector layer, and a single layer configuration may be adopted.

In addition, the positive electrode active material layer generally contains a solid electrolyte (preferably an inorganic solid electrolyte) together with a positive electrode active material, but may not contain the solid electrolyte.

In a case where the positive electrode active material layer contains a solid electrolyte, the type of the solid electrolyte is not particularly limited. From the viewpoint of achieving both flexibility and safety at a high level, it is preferable to use the above-described solid electrolyte (I). In this manner, the solid electrolyte (I) also acts as a binder of solid particles contained in the positive electrode layer, and thus the positive electrode layer can be made to have higher flexibility.

The positive electrode active material layer may contain one or two or more kinds of solid electrolytes.

A content of the solid electrolyte in the positive electrode active material layer is not particularly limited, and is preferably 50% to 99.9% by mass, more preferably 70% to 99.5% by mass, and still more preferably 90% to 99% by mass, as the total content of the solid electrolyte and the positive electrode active material.

As the positive electrode active material used in the positive electrode layer, a positive electrode active material which can be used for a typical lithium ion secondary battery can be widely used. A suitable aspect of the positive electrode active material will be described below.

(Positive Electrode Active Material)

As the positive electrode active material, a positive electrode active material capable of reversibly intercalating and/or deintercalating lithium ions is preferable. The positive electrode active material is not particularly limited, and is preferably a transition metal oxide and more preferably a transition metal oxide containing a transition metal element Ma (one or more kinds of elements selected from Co, Ni, Fe, Mn, Cu, and V). In addition, an element Mb (an element of Group 1 (Ia) of the periodic table other than lithium, an element of Group 2 (IIa), or an element such as Al, Ga, In, Ge, Sn, Pb, Sb, Bi, Si, P, or B) may be mixed into the transition metal oxide. The amount of the Mb mixed is preferably 0 to 30 mol % with respect to the amount (100 mol %) of the transition metal element Ma. It is more preferable that the transition metal oxide is synthesized by mixing the above-described components such that a molar ratio Li/Ma is 0.3 to 2.2.

Specific examples of the transition metal oxide include (MA) transition metal oxides having a bedded salt-type structure, (MB) transition metal oxides having a spinel-type structure, (MC) lithium-containing transition metal phosphoric acid compounds, (MD) lithium-containing transition metal halogenated phosphoric acid compounds, and (ME) lithium-containing transition metal silicate compounds.

Examples of the transition metal oxide having a bedded salt-type structure (MA) include LiCoO₂ (lithium cobalt oxide [LCO]), LiNi₂O₂ (lithium nickelate), LiNi_0.85Co_0.10Al_0.05O₂ (lithium nickel cobalt aluminum oxide [NCA]), LiNi_1/3Co_1/3Mn_1/3O₂ (lithium nickel manganese cobalt oxide [NMC]), and LiNi_0.5Mn_0.5O₂ (lithium manganese nickelate).

Examples of the transition metal oxide having a spinel-type structure (MB) include LiMn₂O₄ (LMO), LiNi_0.5Mn_1.5O₄ ([LNMO]), LiCoMnO₄, Li₂FeMn₃O₈, Li₂CuMn₃O₈, Li₂CrMn₃O₈, and Li₂NiMn₃O₈.

Examples of the lithium-containing transition metal phosphoric acid compound (MC) include olivine-type iron phosphate salts such as LiFePO₄ ([LFP]) and Li₃Fe₂(PO₄)₃; iron pyrophosphates such as LiFeP₂₀₇; cobalt phosphates such as LiCoPO₄; cobalt pyrophosphates such as Li₂CoP₂O₇; and monoclinic NASICON-type vanadium phosphate salts such as Li₃V₂(PO₄)₃ (lithium vanadium phosphate).

Examples of the lithium-containing transition metal halogenated phosphoric acid compound (MD) include iron fluorophosphates such as Li₂FePO₄F, manganese fluorophosphates such as Li₂MnPO₄F, and cobalt fluorophosphates such as Li₂CoPO₄F.

Examples of the lithium-containing transition metal silicate compound (ME) include Li₂FeSiO₄, Li₂MnSiO₄, and Li₂CoSiO₄.

A shape of the positive electrode active material is not particularly limited, and is typically a particle shape. A volume average particle size of the positive electrode active material is not particularly limited, and is, for example, preferably 0.1 to 50 μm. The volume average particle size of the positive electrode active material can be determined in the same manner as the volume average particle diameter of the negative electrode active material, which will be described later.

A positive electrode active material obtained using a baking method may be used after being washed with water, an acidic aqueous solution, an alkaline aqueous solution, or an organic solvent.

The positive electrode active material may be surface-coated with a surface coating agent, sulfur, or phosphorus, and further with actinic ray, same as the negative electrode active material described later.

One kind of the positive electrode active material may be used alone, or two or more kinds thereof may be used in combination.

A content of the positive electrode active material in the positive electrode active material layer is not particularly limited, and is preferably 10% to 97% by mass, more preferably 30% to 95% by mass, still more preferably 40% to 93% by mass, and particularly preferably 50% to 90% by mass.

Among these, as the positive electrode active material, LiCoO₂ (LCO), LiNi_1/3Co_1/3Mn_1/3O₂ (NCM), LiFePO₄ (LFP), LiMn₂O₄ (LMO), LiNi_0.5Mn_1.5O₄ (LNMO), Li₂CoP₂O₇, or an active material in which these substances are coated with an interface resistance-stabilizing layer such as an oxide and a carbon-based material, which will be described later, is preferable.

(Positive Electrode Collector Layer)

The collector layer constituting the positive electrode layer is an electron conductor. In addition, the positive electrode collector layer is usually in a form of a film sheet.

Examples of a constitutional material of the positive electrode collector layer include aluminum (Al), an aluminum alloy (Al alloy), copper (Cu), stainless steel, nickel, and titanium; and aluminum, an aluminum alloy, copper (Cu), or titanium is preferable and aluminum, an aluminum alloy, or copper (Cu) is more preferable.

Examples of the positive electrode collector layer also include a collector layer having a coating layer (thin film) of carbon, nickel, titanium, aluminum, or silver on a surface of aluminum or stainless steel.

Examples of the above-described Al alloy include an Al—Cu-based alloy (approximately 500° C. to 640° C.), an Al—Mn-based alloy (approximately 640° C.), an Al—Si-based alloy (approximately 530° C. to 570° C.), an Al—Mg-based alloy (approximately 570° C. to 650° C.), an Al—Mg—Si-based alloy (approximately 580° C. to 650° C.), and an Al—Zn—Mg-based alloy (approximately 480° C. to 640° C.). Temperatures in the parentheses all mean a melting point at normal pressure.

A thickness of the positive electrode active material layer constituting the secondary battery according to the embodiment of the present invention is not particularly limited, and can be set to, for example, 5 to 500 μm, preferably 20 to 200 μm. In addition, for example, the thickness thereof can be set to 0.1 to 50 μm, and in this case, it is preferably 1 to 20 μm.

In addition, a thickness of the positive electrode collector layer constituting the secondary battery according to the embodiment of the present invention is not particularly limited, and can be set to, for example, 10 to 100 μm, preferably 10 to 50 μm. In addition, for example, the thickness thereof can be set to 0.01 to 20 μm, and in this case, it is preferably 0.05 to 10 μm and more preferably 0.1 to 5 μm.

<Negative Electrode Layer>

The negative electrode layer generally includes a negative electrode collector layer and a negative electrode active material layer, but may be composed of the negative electrode active material layer, not including the negative electrode collector layer. In other words, in a case where the negative electrode active material layer also functions as the negative electrode collector layer, it is not necessary to be composed of two layers of the negative electrode active material layer and the negative electrode collector layer, and a single layer configuration may be adopted.

In addition, the negative electrode active material layer generally contains a solid electrolyte (preferably an inorganic solid electrolyte) together with a negative electrode active material, but may not contain the solid electrolyte.

In a case where the negative electrode active material layer contains a solid electrolyte, the type of the solid electrolyte is not particularly limited. From the viewpoint of achieving both flexibility and safety at a high level, it is preferable to use the above-described solid electrolyte (I). In this manner, the solid electrolyte (I) also acts as a binder of solid particles contained in the negative electrode layer, and thus the negative electrode layer can be made to have higher flexibility.

The negative electrode active material layer may contain one or two or more kinds of solid electrolytes.

A content of the solid electrolyte in the negative electrode active material layer is not particularly limited, and is preferably 50% to 99.9% by mass, more preferably 70% to 99.5% by mass, and still more preferably 90% to 99% by mass, as the total content of the solid electrolyte and the negative electrode active material.

As the negative electrode active material used in the negative electrode layer, a negative electrode active material which can be used for a typical lithium ion secondary battery can be widely used. A suitable aspect of the negative electrode active material will be described below.

(Negative Electrode Active Material)

As the negative electrode active material, a negative electrode active material capable of reversibly intercalating and deintercalating lithium ions is preferable. The negative electrode active material is not particularly limited, and examples thereof include a carbonaceous material, an oxide of a metal element or a metalloid element, a lithium single substance, a lithium alloy, and a negative electrode active material capable of forming an alloy with lithium.

The carbonaceous material used as the negative electrode active material is a material substantially consisting of carbon. Examples thereof include petroleum pitch; carbon black such as acetylene black (AB); graphite (natural graphite and artificial graphite such as vapor-grown graphite); and carbonaceous material obtained by baking various synthetic resins such as a polyacrylonitrile (PAN)-based resin and a furfuryl alcohol resin.

Furthermore, examples thereof also include various carbon fibers such as PAN-based carbon fiber, cellulose-based carbon fiber, pitch-based carbon fiber, vapor-grown carbon fiber, dehydrated polyvinyl alcohol (PVA)-based carbon fiber, lignin carbon fiber, vitreous carbon fiber, and activated carbon fiber; mesophase microspheres, graphite whisker, and tabular graphite.

These carbonaceous materials can be classified into non-graphitizable carbonaceous materials (also referred to as “hard carbon”) and graphitizable carbonaceous materials, based on the graphitization degree.

In addition, it is preferable that the carbonaceous material has a surface spacing, density, or crystallite size described in JP1987-022066A (JP-S62-022066A), JP1990-006856A (JP-H2-006856A), and JP1991-045473A (JP-H3-045473A). The carbonaceous material is not necessarily a single material, and for example, may be a mixture of natural graphite and artificial graphite described in JP1993-090844A (JP-H5-090844A) or graphite having a coating layer described in JP1994-004516A (JP-H6-004516A).

The carbonaceous material is preferably hard carbon or graphite, and more preferably graphite.

The oxide of a metal element or a metalloid element, which can be used as the negative electrode active material, is not particularly limited as long as it is an oxide capable of intercalating and deintercalating lithium; and examples thereof include an oxide of a metal element (metal oxide) such as Fe₃O₄, a composite oxide of a metal element, a composite oxide of a metal element and a metalloid element, and an oxide of a metalloid element (a metalloid oxide). The composite oxide of a metal element and the composite oxide of a metal element and a metalloid element are also collectively referred to as a metal composite oxide.

These oxides are preferably a noncrystalline oxide, and also preferably a chalcogenide which is a reaction product between a metal element and an element of Group 16 of the periodic table.

In the present invention, the metalloid element refers to an element having intermediate properties between those of a metal element and a non-metalloid element, and typically, the metalloid element includes six elements including boron, silicon, germanium, arsenic, antimony, and tellurium, and further includes three elements including selenium, polonium, and astatine.

In addition, the “noncrystalline” means an oxide having a broad scattering band with an apex in a range of 20° to 40° in terms of the 2θ value in case of being measured by an X-ray diffraction method using a CuKα ray, and the oxide may have a crystalline diffraction line. The highest intensity in a crystalline diffraction line observed in a range of 40° to 70° in terms of the 2θ value is preferably 100 times or less and more preferably 5 times or less with respect to the intensity of a diffraction line at the apex in a broad scattering band observed in a range of 20° to 40° in terms of the 2θ value, and it is still more preferable that the oxide does not have a crystalline diffraction line.

In the compound group consisting of the noncrystalline oxides and the chalcogenides described above, the noncrystalline oxide of a metalloid element or the above-described chalcogenide is more preferable; and a (composite) oxide consisting of one element or a combination of two or more elements selected from elements (for example, Al, Ga, Si, Sn, Ge, Pb, Sb, and Bi) of Group 13 (IIIB) to Group 15 (VB) of the periodic table or the chalcogenide is particularly preferable.

The noncrystalline oxide and the chalcogenide are preferably Ga₂O₃, GeO, PbO, PbO₂, Pb₂O₃, Pb₂O₄, Pb₃O₄, Sb₂O₃, Sb₂O₄, Sb₂O₈Bi₂O₃, Sb₂O₈Si₂O₃, Sb₂O₅, Bi₂O₃, Bi₂O₄, GeS, PbS, PbS₂, Sb₂S₃, or Sb₂S₅.

As a negative electrode active material which can be used in combination with the noncrystalline oxide negative electrode active material mainly using Sn, Si, or Ge, a carbonaceous material capable of intercalating and deintercalating lithium ions or lithium metal, a lithium single substance, a lithium alloy, or a negative electrode active material capable of forming an alloy with lithium is preferable.

From the viewpoint of high current density charging and discharging characteristics, it is preferable that the oxide of a metal element or a metalloid element (particularly, the metal (composite) oxide) and the above-described chalcogenide contains at least one of titanium or lithium as a constitutional component.

Examples of the metal composite oxide containing lithium (lithium composite metal oxide) include a composite oxide of lithium oxide and the above-described metal composite oxide or the above-described chalcogenide. More specific examples thereof include Li₂SnO₂.

It is also preferable that the negative electrode active material (for example, the metal oxide) contains a titanium element (a titanium oxide). Specifically, Li₄Ti₅O₁₂ (lithium titanium oxide [LTO]) is preferable from the viewpoint that the volume variation during the intercalation and deintercalation of lithium ions is small, and thus high-speed charging and discharging characteristics are excellent, and deterioration of electrodes is suppressed, whereby it is possible to improve life of the all-solid-state lithium ion secondary battery.

The lithium alloy as the negative electrode active material is not particularly limited as long as it is typically used as a negative electrode active material for an all-solid-state lithium ion secondary battery, and examples thereof include a lithium aluminum alloy.

The negative electrode active material capable of forming an alloy with lithium is not particularly limited as long as it is typically used as a negative electrode active material for an all-solid-state lithium ion secondary battery. Examples of the above-described negative electrode active material include a negative electrode active material (alloy) containing a silicon element or a tin element and a metal such as Al and In; and a negative electrode active material containing a silicon element (silicon element-containing active material) capable of exhibiting high battery capacity is preferable, and a silicon element-containing active material in which a content of the silicon element is 50 mol % or more with respect to all constitutional elements is more preferable.

In general, a negative electrode containing the negative electrode active material (for example, an Si negative electrode containing the silicon element-containing active material or an Sn negative electrode containing an active material containing a tin element) can intercalate a larger amount of Li ions than a carbon negative electrode (for example, graphite or acetylene black). That is, the amount of Li ions intercalated per unit mass increases. Therefore, it is possible to increase the battery capacity. As a result, there is an advantage in that the battery driving duration can be extended.

Examples of the silicon element-containing active material include a silicon-containing alloy (for example, LaSi₂, VSi₂, La—Si, Gd—Si, or Ni—Si) containing a silicon material such as Si and SiO_x (0<x≤1) and further containing titanium, vanadium, chromium, manganese, nickel, copper, or lanthanum; and a structured active material thereof (for example, LaSi₂/Si). In addition, examples thereof include an active material containing a silicon element and a tin element, such as SnSiO₃ and SnSiS₃. Since SiO_x itself can be used as the negative electrode active material (the metalloid oxide) and Si is produced along with the operation of the all-solid-state lithium ion secondary battery, SiO_x can be used as a negative electrode active material (or a precursor material thereof) capable of forming an alloy with lithium.

Examples of the negative electrode active material containing a tin element include Sn, SnO, SnO₂, SnS, SnS₂, and the above-described active material containing a silicon element and a tin element.

From the viewpoint of battery capacity, the negative electrode active material is preferably the negative electrode active material capable of forming an alloy with lithium, more preferably the above-described silicon material or the above-described silicon-containing alloy (alloy containing a silicon element), and still more preferably silicon (Si) or a silicon-containing alloy.

It is also preferable to use a titanium niobium composite oxide as the negative electrode active material. It is expected that the titanium niobium composite oxide has a high theoretical volume capacity density, long life, and possibility of rapid charging. Examples of the titanium niobium composite oxide include TiNb₂O₇ ([TNO]).

A shape of the negative electrode active material is not particularly limited, but is preferably a particle shape. A volume average particle size of the negative electrode active material is not particularly limited, and it is preferably 0.1 to 60 μm, more preferably 0.5 to 20 μm, and still more preferably 1.0 to 15 μm.

The volume average particle size is measured according to the following procedure.

Using water (in a case of being unstable in water, heptane), the negative electrode active material is diluted in a 20 mL sample bottle to prepare a 1% by mass dispersion liquid. The diluted dispersion liquid sample is irradiated with 1 kHz ultrasonic waves for 10 minutes, and then immediately used for test. Data collection is performed 50 times with the dispersion liquid sample using a laser diffraction/scattering-type particle size distribution analyzer and a quartz cell for measurement at a temperature of 25° C., thereby obtaining the volume average particle size. Other detailed conditions and the like can be found in JIS Z 8828:2013 “Particle Diameter Analysis-Dynamic Light Scattering”, as necessary. Five samples are produced for each level, and the average value thereof is adopted.

One kind of the negative electrode active material may be used alone, or two or more kinds thereof may be used in combination.

A content of the negative electrode active material in the negative electrode active material layer is not particularly limited, and is preferably 10% to 90% by mass, more preferably 20% to 85% by mass, still more preferably 30% to 80% by mass, and particularly preferably 35% to 75% by mass.

A surface of the negative electrode active material may be coated with an oxide such as another metal oxide and a carbon-based material. These surface coating layers can function as an interface resistance-stabilizing layer.

Examples of the surface coating agent include a metal oxide containing Ti, Nb, Ta, W, Zr, Al, Si, or Li. Examples thereof include titanium oxide spinel, tantalum-based oxides, niobium-based oxides, and lithium niobate-based compounds; and specific examples thereof include Li₄Ti₅O₁₂, Li₂Ti₂O₅, LiTaO₃, LiNbO₃, LiAlO₂, Li₂ZrO₃, Li₂WO₄, Li₂TiO₃, Li₂B₄O₇, Li₃PO₄, Li₂MoO₄, Li₃BO₃, LiBO₂, Li₂CO₃, Li₂SiO₃, SiO₂, TiO₂, ZrO₂, Al₂O₃, B₂O₃, and Li₃AlF₆. In addition, a carbon-based material such as C, SiC, and SiOC (carbon-added silicon oxide) can also be used as the surface coating material.

In addition, the surface of the negative electrode active material may be subjected to a surface treatment with sulfur or phosphorus.

Furthermore, the surface of the negative electrode active material may be subjected to a surface treatment with an actinic ray or an active gas (for example, plasma) before or after the above-described surface coating.

Among these, as the negative electrode active material, TiNb₂O₇ (TNO), Li₄Ti₅O₁₂ (LTO), Fe₃O₄, or an active material in which these substances are coated with the interface resistance-stabilizing layer such as an oxide and a carbon-based material is preferable.

(Negative Electrode Collector Layer)

The collector layer constituting the negative electrode layer is an electron conductor. In addition, the negative electrode collector layer is usually in a form of a film sheet.

Examples of a constitutional material of the negative electrode collector layer include aluminum, an aluminum alloy, copper, a copper alloy, stainless steel, nickel, zinc, and titanium; and aluminum, an aluminum alloy, or copper is preferable.

Examples of the negative electrode collector layer also include a collector layer having a coating layer (thin film) of carbon, nickel, zinc, titanium, aluminum, gold, or silver on a surface of aluminum, copper, a copper alloy, or stainless steel.

A thickness of the negative electrode active material layer constituting the secondary battery according to the embodiment of the present invention is not particularly limited, and can be set to, for example, 5 to 500 μm, preferably 20 to 200 μm. In addition, for example, the thickness thereof can be set to 0.1 to 50 μm, and in this case, it is preferably 1 to 20 μm.

In addition, a thickness of the negative electrode collector layer constituting the secondary battery according to the embodiment of the present invention is not particularly limited, and can be set to, for example, 10 to 100 μm, preferably 10 to 50 μm. In addition, for example, the thickness thereof can be set to 0.01 to 20 μm, and in this case, it is preferably 0.05 to 10 μm and preferably 0.1 to 5 μm.

(Collector Layer in Secondary Battery According to Embodiment of Present Invention)

In the secondary battery according to the embodiment of the present invention, at least one of the positive electrode layer or the negative electrode layer includes a collector layer, and at least one collector layer is a layer having, as a constitutional material, a metal melted at 670° C. under normal pressure or a layer having the metal in a coating layer.

In the present invention or the specification, the “metal melted at 670° C. under normal pressure” means a metal which is melted at 670° C. under a pressure condition of 101.33 kPa, and means a metal having a melting point of 670° C. or lower under normal pressure.

Specific examples of the “metal melted at 670° C. under normal pressure” include Al (melting point under normal pressure: approximately 650° C. to 660° C.) and an Al alloy (melting point under normal pressure: approximately 480° C. to 650° C.) described in the positive electrode collector layer above; and Al (melting point under normal pressure: approximately 650° C. to 660° C.) described in the negative electrode collector layer above.

In the all-solid-state lithium ion secondary battery using the oxide-based solid electrolyte in the related art, aluminum or an aluminum alloy may be used as a constitutional material of the collector layer or a material used in the coating layer. However, as described above, since the high-temperature sintering treatment is essential in the oxide-based solid electrolyte in the related art, in practice, the all-solid-state lithium ion secondary battery using the oxide-based solid electrolyte in the related art, which has a collector layer having aluminum or an aluminum alloy as a constituent material or a collector layer having the metal in the coating layer, has not been able to exist.

The positive electrode layer and the negative electrode layer may contain a component (other components) other than the solid electrolyte and the active material in the active material layers. For example, a conductive auxiliary agent can be contained.

As the conductive auxiliary agent, a conductive auxiliary agent which is known as a general conductive auxiliary agent can be used. Examples of the conductive auxiliary agent include graphite such as natural graphite and artificial graphite, carbon black such as acetylene black, Ketjen black, and furnace black, amorphous carbon such as needle cokes, carbon fiber such as vapor-grown carbon fiber and carbon nanotube, and a carbonaceous material such as graphene and fullerene, which are electron-conductive materials. Furthermore, a conductive polymer such as polyaniline, polypyrrole, polythiophene, polyacetylene, and a polyphenylene derivative may also be used.

In addition to the above-described conductive auxiliary agent, a general conductive auxiliary agent containing no carbon atom, such as metal powder and metal fiber, may be used.

The conductive auxiliary agent refers to a conductive auxiliary agent which does not cause the intercalation and deintercalation of Li at the time of charging and discharging of the battery, and does not function as an active material. As a result, among conductive auxiliary agents, a conductive auxiliary agent which can function as the active material in the active material layer at the time of charging and discharging of the battery is classified as the active material, not as the conductive auxiliary agent. Whether or not the conductive auxiliary agent functions as the active material at the time of charging and discharging of the battery is not unambiguously determined, and determined by a combination with the active material.

A content of the conductive auxiliary agent in the positive electrode active material layer is not particularly limited, and it is, for example, preferably 0% to 10% by mass and more preferably 1% to 5% by mass.

A content of the conductive auxiliary agent in the negative electrode active material layer is not particularly limited, and it is, for example, preferably 0% to 10% by mass and more preferably 1% to 5% by mass.

Examples of the other components also include the above-described binder and lithium salt.

<Manufacturing of all-Solid-State Lithium Ion Secondary Battery>

The secondary battery according to the embodiment of the present invention can be manufactured with reference to a general manufacturing method for an all-solid-state secondary battery, except that the solid electrolyte (I) is used in at least the solid electrolyte layer, at least one of the positive electrode layer or the negative electrode layer includes a collector layer, and a layer having a specific metal as a constitutional material or a layer having the metal in a coating layer is used as at least one collector layer. That is, the manufacturing method of the secondary battery according to the embodiment of the present invention can be performed by including a step of obtaining a laminate in which a positive electrode layer, a solid electrolyte layer, and a negative electrode layer are arranged in this order. Here, an amount of water used in the solid electrolyte (I) may satisfy or not satisfy the amount specified in the present invention. In a manufacturing method of an all-solid-state secondary battery, the amount of water used in the solid electrolyte (I) is not regarded; but in order to set the amount of water of the solid electrolyte (I) contained in the constitutional layer such as the solid electrolyte layer to the amount specified in the present invention, in the manufacturing of the secondary battery according to the embodiment of the present invention, a step of subjecting the formed solid electrolyte layer to a drying treatment can also be included as necessary. The drying step of the constitutional layer such as the solid electrolyte layer may be performed at any stage after the constitutional layer such as the solid electrolyte layer is formed, as long as the solid electrolyte (I) of the constitutional layer such as the solid electrolyte layer in the secondary battery to be obtained can be set to the water amount specified in the present invention. In order to more reliably set the water amount specified in the present invention, it is preferable to performing the drying treatment on the laminate in which the positive electrode layer, the solid electrolyte layer, and the negative electrode layer are arranged in this order at least a state in which the laminate is disposed in a battery cell. The drying method is not particularly limited, and for example, the water amount of the solid electrolyte (I) in the solid electrolyte layer can be reduced to within the range specified in the present invention by using a desiccator, subjecting the solid electrolyte layer to vacuum drying, subjecting the solid electrolyte layer to freeze vacuum drying, or subjecting the solid electrolyte layer to a heating treatment.

The secondary battery according to the embodiment of the present invention is preferably obtained by sealing the above-described laminate in which the positive electrode layer, the solid electrolyte layer, and the negative electrode layer are arranged in this order. By the sealing, it is possible to more reliably prevent the mixing of moisture into the solid electrolyte layer after the above-described drying step, and thus it is possible to further improve the cycle characteristics. The sealing method is not particularly limited as long as the mixing of moisture (atmosphere) can be blocked or suppressed. Examples thereof include a method of sealing the above-described laminate in which the positive electrode layer, the solid electrolyte layer, and the negative electrode layer are arranged in this order by closing a lid of a housing (battery cell) storing the laminate using a gasket such as an O-ring. Furthermore, cell resistance can also be improved by heating the obtained laminate (for example, at 80° C. for 2 hours).

In one aspect of the manufacturing method of the secondary battery according to the embodiment of the present invention, at least one collector layer included in at least one of the positive electrode layer or the negative electrode layer is a layer having, as a constitutional material, a metal melted at 670° C. under normal pressure or a layer having the metal in a coating layer.

As described above, in the secondary battery according to the embodiment of the present invention, since at least the solid electrolyte layer contains the solid electrolyte (I) and the high-temperature sintering treatment is not required, as the metal used as a constitutional material of the collector layer or contained in the coating layer, a metal melted at 670° C. under normal pressure, which is difficult to use in the oxide-based solid electrolyte in the related art, can be used. The metal melted at 670° C. under normal pressure is as described above.

In addition, in another aspect of the manufacturing method of the secondary battery according to the embodiment of the present invention, at least one collector layer included in at least one of the positive electrode layer or the negative electrode layer is a layer having Cu as a constitutional material or a layer having Cu in a coating layer, and the laminate of the positive electrode layer, the solid electrolyte layer, and the negative electrode layer is manufactured at 300° C. or lower in an atmosphere containing oxygen gas.

As described above, in the secondary battery according to the embodiment of the present invention, since at least the solid electrolyte layer contains the solid electrolyte (I) and the high-temperature sintering treatment is not required, as the metal used as a constitutional material of the collector layer or contained in the coating layer, Cu oxidized under high temperature conditions with oxygen gas, which is difficult to use in the oxide-based solid electrolyte in the related art, can be used even in an atmosphere containing oxygen gas. In a case of manufacturing at 300° C. or lower in the atmosphere containing oxygen gas, oxidation of Cu can be suppressed depending on conditions such as a heating time and a heating temperature. Examples of the atmosphere containing oxygen gas generally include air. A content concentration of the oxygen gas is not particularly limited, and the upper limit value thereof can be set to 100 vol % or less and the lower limit value thereof can be set to, for example, 1 vol % or more.

The expression of “manufactured at 300° C. or lower” essentially means that a sintering treatment step at a high temperature, which is essential for the oxide-based solid electrolyte in the related art, is not required. In the present invention, the secondary battery according to the embodiment of the present invention can be manufactured by a manufacturing step at 300° C. or lower in an atmosphere containing oxygen gas, and it can be manufactured in an atmosphere containing oxygen gas, preferably at 200° C. or lower, more preferably 120° C. or lower, and still more preferably 100° C. or lower. Among these, the manufacturing can be performed in an atmosphere containing oxygen gas, preferably at 80° C. or lower, more preferably 60° C., still more preferably 40° C., and particularly preferably under a condition in which heating is not performed (for example, room temperature of 20° C. to 27° C.).

In addition, a method of forming the laminate in which the positive electrode layer, the solid electrolyte layer, and the negative electrode layer are arranged in this order is not particularly limited.

Examples of the manufacturing method of the all-solid-state secondary battery include a method in which a composition for forming a positive electrode (positive electrode slurry) containing a positive electrode active material is applied onto a metal foil which is a positive electrode collector layer to form a positive electrode active material layer, a dispersion liquid for forming a solid electrolyte layer (solid electrolyte slurry) containing a solid electrolyte is applied onto the positive electrode active material layer to form a solid electrolyte layer, a composition for forming a negative electrode (negative electrode slurry) containing a negative electrode active material is applied onto the solid electrolyte layer to form a negative electrode active material layer, and a negative electrode collector layer (metal foil) is laminated on the negative electrode active material layer. The entire laminate is optionally subjected to a pressurization treatment to obtain the all-solid-state lithium ion secondary battery as shown in FIG. 1.

In addition, the all-solid-state lithium ion secondary battery can also be manufactured by reversing the method of forming each layer, which includes forming the negative electrode active material layer, the solid electrolyte layer, and the positive electrode active material layer on the negative electrode collector layer, laminating the positive electrode collector layer (metal foil) on the positive electrode active material layer, and optionally subjecting the entire laminate to a pressurization treatment.

As another method, the all-solid-state lithium ion secondary battery can also be manufactured by separately producing the positive electrode active material layer, the solid electrolyte layer, and the negative electrode active material layer, laminating these layers between the positive electrode collector layer and the negative electrode collector layer to be arranged in order of the positive electrode collector layer (metal foil), the positive electrode active material layer, the solid electrolyte layer, the negative electrode active material layer, and the negative electrode collector layer (metal foil), and optionally subjecting to a pressurization treatment.

In this case, in the formation of each layer, a support such as a nonwoven fabric may be disposed as necessary, and each layer can be made into a self-supporting film. In a case where the all-solid-state lithium ion secondary battery is manufactured by laminating the respective layers, the support in the self-supporting film is preferably removed and used.

As another method, the all-solid-state lithium ion secondary battery can also be manufactured by pressurizing each of powders constituting each of the layers to have a predetermined shape to form pellets of each of the layers, and superimposing pellets on a collector layer of a positive electrode or a negative electrode and pressurizing the pellets. In this case, a powder constituting the positive electrode active material layer (hereinafter, referred to as a powder of a positive electrode mixture), a powder constituting the solid electrolyte layer (hereinafter, referred to as a powder of a solid electrolyte), and a powder constituting the negative electrode active material layer (hereinafter, referred to as a powder of a negative electrode mixture) are used.

For example, a pellet of the solid electrolyte is formed by filling a predetermined mold with the powder of the solid electrolyte and performing pressure molding; a pellet of the negative electrode mixture is formed by filling one surface of the obtained pellet of the solid electrolyte with the powder of the negative electrode mixture and performing pressure molding; a pellet of the positive electrode mixture is formed by filling the other surface of the obtained pellet of the solid electrolyte with the powder of the positive electrode mixture and performing pressure molding; and a compacted powder molded body in which the pellet of the positive electrode mixture, the pellet of the solid electrolyte, and the pellet of the negative electrode mixture are laminated in this order is obtained. Subsequently, in the obtained compacted powder molded body, the obtained pellet of the negative electrode mixture is superposed on the negative electrode collector layer (metal foil) such that the pellet is on the lower side, the positive electrode collector layer (metal foil) is superposed on the pellet of the positive electrode mixture such that the pellet is on the upper side, and the entire layer is subjected to a pressurization treatment, thereby obtaining the all-solid-state lithium ion secondary battery as shown in FIG. 1.

A method of preparing the powder of the solid electrolyte is not particularly limited, and for example, the powder can be prepared by freeze vacuum-drying a dispersion liquid (solid electrolyte slurry) for forming a solid electrolyte layer containing a solid electrolyte.

The method of preparing the powder of the negative electrode mixture is not particularly limited, and the powder of the negative electrode mixture can be prepared, for example, by mixing the powder of the solid electrolyte prepared in advance with a component for forming the negative electrode active material layer containing a negative electrode active material.

The method of preparing the powder of the positive electrode mixture is not particularly limited, and the powder of the positive electrode mixture can be prepared, for example, by mixing the powder of the solid electrolyte prepared in advance with a component for forming the positive electrode active material layer containing a positive electrode active material.

Pressurization conditions in a case of producing the pellet of the negative electrode mixture, the pellet of the solid electrolyte, and the pellet of the positive electrode mixture are not particularly limited, and for example, the pellets can be produced by pressurization to a pressure of 50 to 300 MPa for approximately 10 seconds.

In addition, the compression bonding of the pellet of the negative electrode mixture and the negative electrode collector layer and the compression bonding of the pellet of the positive electrode mixture and the positive electrode collector layer can also be performed by pressurization of approximately 60 MPa.

The order of forming the pellets of each layer is not particularly limited, and for example, the pellets can be formed in the order of the pellet of the negative electrode mixture, the pellet of the solid electrolyte, and the pellet of the positive electrode mixture.

As another method, the all-solid-state lithium ion secondary battery can also be manufactured by separately producing the pellet of the negative electrode mixture, the pellet of the solid electrolyte, and the pellet of the positive electrode mixture, superimposing the obtained pellets, and laminating the obtained pellets by pressing the obtained pellets so that the pellets are interposed between the collector layers of the positive electrode and the negative electrode.

In addition, as a manufacturing method of a small-sized laminated battery in which a plurality of positive electrode layers, solid electrolyte layers, and negative electrode layers are laminated with a solid electrolyte layer disposed between adjacent positive electrode layers and negative electrode layers, the small-sized laminated battery can be manufactured with reference to, for example, the lamination method described in paragraphs [0033] to [0046] of JP2016-001602A. As a method of producing each of the positive electrode active material layer, the solid electrolyte layer, and the negative electrode active material layer, each layer can be produced based on the above-described manufacturing method according to the embodiment of the present invention.

The secondary battery according to the embodiment of the present invention is not limited to the above-described methods as long as the secondary battery specified in the present invention can be obtained.

In the manufacturing of the secondary battery according to the embodiment of the present invention, it is possible to form a layer in which the interface resistance between the solid particles or between the layers is suppressed by the action of the above-described oxide-based solid electrolyte (I) capable of being easily plastically deformed with pressure, even in a case where the sulfide-based solid electrolyte is not used as the solid electrolyte.

The solid electrolyte (I) itself is soft and plastically deformed to act as a binder, which contributes to the improvement of bonding property between the solid particles or between the layers, so that it is also possible to form a layer without using a binder such as an organic polymer.

It is preferable that the secondary battery according to the embodiment of the present invention is initialized after manufacturing or before use. The initialization method is not particularly limited, and it is possible to initialize the secondary battery by, for example, performing initial charging and discharging in a state in which a pressing pressure is increased and then releasing the pressure until the pressure falls within the range of the pressure condition at the time of using the secondary battery.

<Applications of all-Solid-State Lithium Ion Secondary Battery>

The secondary battery according to the embodiment of the present invention can be applied to various applications. The application aspect is not particularly limited, and in a case of being mounted in an electronic apparatus, examples thereof include a notebook computer, a pen-based input personal computer, a mobile personal computer, an e-book player, a mobile phone, a cordless phone handset, a pager, a handy terminal, a portable fax, a mobile copier, a portable printer, a headphone stereo, a video movie, a liquid crystal television, a handy cleaner, a portable CD, a mini disc, an electric shaver, a transceiver, an electronic notebook, a calculator, a memory card, a portable tape recorder, a radio, and a backup power supply. Additionally, in a case of being used for consumer applications, examples thereof include an automobile, an electric vehicle, a motor, a lighting instrument, a toy, a game device, a road conditioner, a watch, a strobe, a camera, and a medical device (a pacemaker, a hearing aid, a shoulder massage device, and the like). Furthermore, the secondary battery according to the embodiment of the present invention can be used for various military usages and universe usages. In addition, the secondary battery according to the embodiment of the present invention can also be combined with a solar battery.

EXAMPLES

The present invention will be described in more detail based on Examples, but the present invention is not limited thereto be interpreted. In the present invention, room temperature means 27° C. In addition, the following production of a solid electrolyte or production of a secondary battery was performed in an atmosphere in which moisture and oxygen gas were present in the atmosphere.

Reference Example 1: Production by Steps 0 and 1A to 3A Described Above

Using a ball mill (manufactured by FRITSCH, planetary ball mill P-7), powdery Li₂B₄O₇ crystals (LBO powder) (manufactured by RARE METALLIC Co., Ltd.) were subjected to ball milling under the following conditions, pot: yttria-stabilized zirconia (YSZ) (45 mL), pulverization ball: YSZ (average particle diameter: 5 mm, number of balls: 50 balls), rotation speed: 370 revolutions per minute (rpm), amount of LBO powder: 1 g, atmosphere: air, and treatment time of ball milling: 100 hours, thereby obtaining a fined lithium-containing oxide (hereinafter, also referred to as “fine substance of the lithium-containing oxide”).

0.05 g (which was 5% by mass with respect to the fine substance of the lithium-containing oxide) of LiFSI (chemical formula: Li(FSO₂)₂N) as a lithium salt was added to 1 g of the obtained fine substance of the lithium-containing oxide, and the mixture was further ball-milled for 100 hours. The obtained powder was added to water such that a powder concentration was 42% by mass, and the mixture was subjected to ultrasonic dispersion for 30 minutes. Subsequently, the obtained dispersion liquid was transferred to a glass petri dish, and dried at 120° C. for 2 hours in the air to obtain a film of solid electrolyte. Subsequently, the obtained film was peeled off to obtain a powdery solid electrolyte (I)-1.

<Production and Evaluation of Molded Body of Solid Electrolyte>

The powdery solid electrolyte (I)-1 obtained above was subjected to powder compaction molding at an effective pressure of 220 MPa at 27° C. (room temperature) to obtain a molded body (a compacted powder body 1) of the solid electrolyte. A shape of the compacted powder body 1 was a columnar shape having a diameter of 10 mm and a thickness of 1 mm. As a result of measuring ion conductivity of the obtained compacted powder body 1, the ion conductivity of the compacted powder body 1 was 1.5×10⁻⁴ S/cm at 27° C. and 4.0×10⁻⁴ S/cm at 60° C.

The above-described ion conductivity of the solid electrolyte (I)-1 was calculated by arranging two electrodes consisting of an In foil to sandwich the compacted powder body 1, measuring an alternating current impedance between both In electrodes in a measurement frequency range of 1 Hz to 1 MHz under conditions of a measurement temperature of 27° C. or 60° C. and an applied voltage of 50 mV, and then analyzing the arc diameter of the obtained Cole-Cole plot (Nyquist plot).

An X-ray diffraction measurement of the solid electrolyte (I)-1 was performed using a CuKα ray as described above. The measurement conditions were set to 0.01°/step and 3°/min. As a result, it was clarified that the above-described X-ray diffraction characteristics were satisfied, and it was found that the solid electrolyte (I)-1 was in an amorphous state.

Using the solid electrolyte (I)-1 obtained above, an X-ray total scattering measurement was performed with SPring-8L04B2 (acceleration voltage: 61.4 keV, wavelength: 0.2019 Å). The sample was sealed in a Capton capillary of 2 mmφ or 1 mmφ, and the experiment was performed. The obtained data were subjected to Fourier transform as described above to obtain a reduced pair distribution function.

As a result of the analysis, in the reduced pair distribution function G(r) obtained from the X-ray total scattering measurement, it was confirmed that, in a range where r was 1 to 5 Å, a first peak in which G(r) of the peak top was more than 1.0 and the peak top was located at 1.43 Å and a second peak in which G(r) of the peak top was more than 1.0 and the peak top was located at 2.40 Å were observed.

On the other hand, in the solid electrolyte (I)-1, the peak attributed to the B—O interatomic distance and the B—B interatomic distance, observed in the general lithium tetraborate crystal, was maintained. The general lithium tetraborate crystal has a structure (diborate structure) in which a BO₄ tetrahedron and a BO₃ triangle are present at a ratio of 1:1, and it is presumed that this structure is maintained in the solid electrolyte (I)-1.

A proportion {(Full-width 2 at half maximum/Full-width 1 at half maximum)×100} of a full-width at half maximum (full-width 2 at half maximum) of a peak in which a chemical shift appeared in a range of −100 to +100 ppm in a spectrum obtained in a case where the solid ⁷Li-NMR measurement of the solid electrolyte (I) obtained above was performed at 120° C. with respect to a full-width at half maximum (full-width 1 at half maximum) of a peak in which a chemical shift appeared in a range of −100 to +100 ppm in a spectrum obtained in a case where the solid ⁷Li-NMR measurement of the solid electrolyte (I) obtained above was performed at 20° C. was 33%.

In addition, in a case where the first peak appearing in a range of −100 to +100 ppm in the spectrum obtained in a case where the solid ⁷Li-NMR measurement was performed at 20° C. was waveform-separated, a second peak having a full-width at half maximum of 5 ppm or less appeared in a range with a chemical shift of −3 to +3 ppm, and a proportion of an area intensity of the second peak to an area intensity of the first peak was 4%.

Using the solid electrolyte (I)-1 obtained above, an infrared absorption spectrum measurement was performed under the conditions described above, and as a result, in the obtained infrared absorption spectrum, a value of a ratio of a maximum absorption intensity in a wave number range of 3,000 to 3,500 cm⁻¹ to a maximum absorption intensity in a wave number range of 800 to 1,600 cm⁻¹ was 0.72.

In the Raman spectrum of the solid electrolyte (I)-1 obtained above, the coefficient of determination obtained by performing linear regression analysis according to a least-squares method in a wave number range of 600 to 850 cm⁻¹ was 0.9974.

The mass reduction rate of the solid electrolyte (I)-1 in a case of being heated from 25° C. to 800° C. as described above was 29.8%.

Regarding the analysis of each of elements in the obtained solid electrolyte (I)-1, quantitative analysis was performed by ICP-OES for lithium and boron or by combustion ion chromatography (combustion IC) for fluorine and sulfur, estimation was performed for N from the analytical mass of sulfur in consideration of the amount of each of atoms in the Li salt, the analytical masses of elements other than O were added together for O, and calculation was performed in terms of the difference from the total amount of the powder. The results are shown in the tables below.

Reference Example 2: Production by Steps 1B to 3B and Method 2 Described Above

1 g of the fine substance of the lithium-containing oxide used in Reference Example 1 was added to water such that a concentration of the fine substance was 42% by mass, and the mixture was subjected to ultrasonic dispersion for 30 minutes. 0.05 g (which was 5% by mass with respect to the fine substance of the lithium-containing oxide) of LiFSI (chemical formula: Li(FSO₂)₂N) as a lithium salt was added to the obtained dispersion liquid, and the mixture was further subjected to ultrasonic dispersion for 30 minutes.

The obtained dispersion liquid was transferred to a glass petri dish, and dried at 120° C. for 2 hours in the air to obtain a film of solid electrolyte. Subsequently, the obtained film was peeled off to obtain a powdery solid electrolyte (I)-2. Various evaluations were performed on the solid electrolyte (I)-2 in the air in the same manner as in Reference Example 1. The results are summarized in the tables below.

Reference Example 3: Production by Steps 1B to 3B and Method 3 Described Above

Using a ball mill (manufactured by FRITSCH, planetary ball mill P-7), powdery Li₂B₄O₇ (LBO powder) (manufactured by RARE METALLIC Co., Ltd.) was subjected to ball milling under the following conditions, pot: YSZ (45 mL), pulverization ball: YSZ (average particle diameter: 5 mm, weight: 70 g), rotation speed: 530 revolutions per minute (rpm), amount of LBO powder: 4.2 g, atmosphere: air, and treatment time of ball milling: 100 hours, thereby obtaining a fine substance of a lithium-containing oxide.

The obtained fine substance of the lithium-containing oxide was added to water such that a concentration of the fine substance was 42% by mass, and the mixture was subjected to ultrasonic dispersion for 60 minutes to obtain a dispersion liquid 1.

Next, 3.25 g of LiFSI (chemical formula: Li(FSO₂)₂N) as a lithium salt was added to water such that a concentration was 87% by mass, and the mixture subjected to an ultrasonic treatment for 60 minutes to obtain a solution 2.

The obtained dispersion liquid 1 and solution 2 were mixed, and stirred and mixed with a magnetic stirrer for 60 minutes. Subsequently, the obtained dispersion liquid was vacuum-dried at 40° C. and 10 Pa for 15 hours to obtain a powdery solid electrolyte (I)-3. The obtained powder was allowed to stand in the air for a certain period of time, and various evaluations were performed in the air in the same manner as in Reference Example 1 using the solid electrolyte (I)-3. The results are summarized in the tables below.

Reference Example 4: Production by Steps 1B to 3B and Method 3 Described Above

A dispersion liquid 3 was obtained in the same manner as in the preparation of the dispersion liquid 1 in Reference Example 3.

Next, 2.32 g of LiFSI (chemical formula: Li(FSO₂)₂N) as a lithium salt was added to water such that a concentration was 87% by mass, and the mixture subjected to an ultrasonic treatment for 60 minutes to obtain a solution 4.

The obtained dispersion liquid 3 and solution 4 were mixed, and stirred and mixed with a magnetic stirrer for 60 minutes. Subsequently, the obtained dispersion liquid was vacuum-dried at 40° C. and 10 Pa for 15 hours to obtain a powdery solid electrolyte (I)-4. The obtained powder was allowed to stand in the air for a certain period of time, and various evaluations were performed in the air in the same manner as in Reference Example 1 using the solid electrolyte (I)-4. The results are summarized in the tables below.

Reference Example 5: Production by Steps 1B to 3B and Method 3 Described Above

A dispersion liquid 5 was obtained in the same manner as in the preparation of the dispersion liquid 1 in Reference Example 3.

Next, 4.65 g of LiFSI (chemical formula: Li(FSO₂)₂N) as a lithium salt was added to water such that a concentration was 87% by mass, and the mixture subjected to an ultrasonic treatment for 60 minutes to obtain a solution 6.

The obtained dispersion liquid 5 and solution 6 were mixed, and stirred and mixed with a magnetic stirrer for 60 minutes. Subsequently, the obtained dispersion liquid was vacuum-dried at 40° C. and 10 Pa for 15 hours to obtain a powdery solid electrolyte (I)-5. Various evaluations were performed in the air in the same manner as in Reference Example 1 using the obtained powdery solid electrolyte (I)-5 as soon as possible. The results are summarized in the tables below.

Reference Example 6: Production by Steps 1B to 3B and Method 3 Described Above

A dispersion liquid 7 was obtained in the same manner as in the preparation of the dispersion liquid 1 in Reference Example 3.

Next, 7.13 g of LiTFSI (chemical formula: Li(F₃CSO₂)₂N) as a lithium salt was added to water such that a concentration was 87% by mass, and the mixture subjected to an ultrasonic treatment for 60 minutes to obtain a solution 8.

The obtained dispersion liquid 7 and solution 8 were mixed, and stirred and mixed with a magnetic stirrer for 60 minutes. Subsequently, the obtained dispersion liquid was vacuum-dried at 40° C. and 10 Pa for 15 hours to obtain a powdery solid electrolyte (I)-6. The obtained powder was allowed to stand in the air for a certain period of time, and various evaluations were performed in the air in the same manner as in Reference Example 1 using the solid electrolyte (I)-6. The results are summarized in the tables below.

In Reference Example 6, the carbon amount shown in Table 1 below was estimated from the analytical mass of sulfur in consideration of the amount of each of atoms in the lithium salt.

Comparative Reference Example 1

As a result of performing the element analysis on the LBO powder used in Reference Example 1 (powdery Li₂B₄O₇ crystals not subjected to the ball milling), the composition of the obtained LBO powder was Li_1.96B_4.00O_6.80. The LBO powder was subjected to powder compaction molding at an effective pressure of 220 MPa at room temperature (27° C.) to obtain a compacted powder body C1 for comparative reference. The ion conductivity of the obtained compacted powder body C1 could not be detected.

In addition, in the same manner as in Reference Example 1, the X-ray total scattering measurement was performed using the LBO powder to obtain a reduced pair distribution function G(r). FIG. 10 shows the reduced pair distribution function G(r) obtained from an X-ray total scattering measurement.

As a result of analysis, in the reduced pair distribution function G(r) of the LBO powder obtained from the X-ray total scattering measurement, a first peak (corresponding to the B—O proximity) in which a peak top was located at 1.40 Å and a second peak (corresponding to the B—B proximity) in which a peak top was located at 2.40 Å were present, and both of G(r) of the peak top of the first peak and G(r) of the peak top of the second peak were 1.0 or more (see FIG. 10). In addition, other peaks in which peak tops were located at 3.65 Å, 5.22 Å, 5.51 Å, and 8.54 Å were present, and the absolute value of G(r) of the peak top of each of the peaks was clearly more than 1.0 (see FIG. 10).

The LBO powder of Comparative Reference Example 1 was subjected to X-ray diffraction measurement using a CuKα ray. The measurement conditions were set to 0.01°/step and 3°/min.

FIG. 11 shows an X-ray diffraction pattern of the LBO powder of Comparative Reference Example 1. As shown in FIG. 11, a plurality of peaks having a small width were observed in the LBO powder used in Comparative Reference Example 1. More specifically, the strongest peak corresponding to (1,1,2) plane was observed at a position of 21.78° in terms of the 2θ value. Other major diffraction peaks observed were a peak corresponding to (2,0,2) plane at a position of 25.54°, a peak corresponding to (2,1,3) plane at a position of 33.58°, and a peak corresponding to (3,1,2) plane at a position of 34.62°; and intensities of these three peaks were substantially the same. These peaks were derived from the crystalline component. [Comparative Reference Example 2]

As a result of the element analysis of the fine substance of the lithium-containing oxide (powdery Li₂B₄O₇ crystals subjected to ball milling) prepared in Reference Example 1, the composition of the fine substance of the lithium-containing oxide was Li_1.94B_4.00O_6.80.

Next, the above-described fine substance of the lithium-containing oxide was subjected to powder compaction molding at an effective pressure of 220 MPa at 27° C. (room temperature) to obtain a compacted powder body (compact powder body R1) for comparative reference. The ion conductivity of the obtained compacted powder body R1 was 7.5×10⁻⁹ S/cm at 27° C. and 7.5×10⁻⁸ S/cm at 60° C.

In the column of “Short distance G(r)” of the tables below, with regard to the reduced pair distribution function G(r) of the solid electrolyte (I) obtained from an X-ray total scattering measurement as described above, a case where a first peak in which a peak top was located in a range where r is 1.43±0.2 Å and a second peak in which a peak top was located in a range where r is 2.40±0.2 Å were present, and both G(r) of the peak top of the first peak and G(r) of the peak top of the second peak were more than 1.0 is indicated by “A”, and other cases are indicated by “B”.

In Reference Examples 1 to 5 and 9 to 13 shown in the tables below, the value of G(r) of the peak top of the first peak was 1.2 or more.

In addition, in the column of “Long distance G(r)”, with regard to the above-described reduced pair distribution function G(r), a case where the absolute value of G(r) was less than 1.0 in a range where r was more than 5 Å and 10 Å or less is indicated by “A”, and a case where the absolute value of G(r) was not less than 1.0 is indicated by “B”.

In addition, as a result of the above-described X-ray diffraction characteristics using a CuKα ray, a case where the above-described X-ray diffraction characteristics were satisfied was indicated by “A”, and a case where the above-described X-ray diffraction characteristics were not satisfied was indicated by “B”. In Reference Examples 1 to 6 shown in the tables below and Reference Examples 7 to 13 described later, in the X-ray diffraction pattern, none of the first peak, the second peak, the third peak, and the fourth peak were present, or the intensity ratio of at least one peak of the first peak, the second peak, the third peak, or the fourth peak was 2.0 or less.

In the tables below, the column of “Element analysis” indicates the molar content amount of each element as a relative value in which the content of B was set to “4.00”, in the composition of the solid electrolyte (I) obtained in each of Reference Examples and the lithium-containing oxide in each of Comparative Reference Examples.

In the tables below, a blank means that the corresponding element was not contained.

In the tables below, “Proportion of full-width at half maximum (%)”, “Coefficient of determination”, and “Mass reduction rate (%)” are as described above in Reference Example 1.

In the tables below, “Proportion of area intensity” is a proportion of the area intensity of the second peak to the area intensity of the first peak in the above-described solid ⁷Li-NMR measurement, and the evaluation results based on the following standards are described.

<Standard for Proportion of Area Intensity>

• • A: case where the proportion of the area intensity was 15% or more
  • B: case where the proportion of the area intensity was 0.5% or more and less than 15%
  • C: case where the proportion of the area intensity was less than 0.5%

In the tables below, the column of “Maximum absorption intensity ratio” indicates whether or not the above-described infrared absorption spectral characteristics were satisfied; and a case where [Maximum absorption intensity in wave number range of 3000 to 3500 cm⁻¹]/[Maximum absorption intensity in wave number range of 800 to 1600 cm⁻¹] was 0.20 or more is indicated by “A”, and a case of being less than 0.20 is indicated by “B”.

In the tables below, “-” means that the measured value is not obtained.

TABLE 1
	Element composition of solid electrolyte
	Li	B	O	F	S	N	C
Reference Example 1	1.94	4.00	10.66	0.03	0.02	0.01
Reference Example 2	2.04	4.00	11.09	0.06	0.05	0.02
Reference Example 3	2.70	4.00	20.90	1.36	1.38	0.69
Reference Example 4	2.50	4.00	19.90	0.95	0.98	0.49
Reference Example 5	3.00	4.00	17.10	1.95	1.98	0.99
Reference Example 6	2.90	4.00	21.45	5.00	1.90	0.95	1.90
Comparative Reference Example 1	1.96	4.00	6.80
Comparative Reference Example 2	1.94	4.00	6.80

TABLE 2
	Proportion	Proportion	Maximum
	of full-width	of	absorption	Coefficient	Mass	Short	Long	X-ray	Ion
	at half	area	intensity	of	reduction	distance	distance	diffraction	conductivity (S/cm)
	maximum (%)	intensity	ratio	determination	rate (%)	G(r)	G(r)	characteristics	27° C.	60° C.
Reference	33	B	A	0.9974	29.8	A	A	A	1.5 × 10−4	4.0 × 10−4
Example 1
Reference	—	A	A	0.9908	30	A	—	A	1.1 × 10−3	4.0 × 10−3
Example 2
Reference	—	A	A	—	—	A	A	A	4.7 × 10−3	—
Example 3
Reference	—	A	A	—	—	A	—	A	4.1 × 10−3	—
Example 4
Reference	—	A	A	—	—	A	—	A	3.0 × 10−3	—
Example 5
Reference	—	B	A	—	—	—	—	A	7.4 × 10−4	—
Example 6
Comparative	100	C	B	0.1660	0.2	A	B	B	Un-	Un-
Reference									detectable	detectable
Example 1
Comparative	46	C	B	0.9677	—	A	A	A	7.5 × 10−9	7.5 × 10−8
Reference
Example 2

As shown in the above tables, it was found that the solid electrolytes (I)-1, (I)-2, (I)-3, (I)-4, (I)-5, and (I)-6 of Reference Examples 1 to 6 had desired characteristics or physical properties, and had excellent ion conductivity. In addition, from the results of the element analysis, it was found that the content of Li in the solid electrolyte was higher in Reference Examples 3 to 6. In Reference Examples 3 to 6, the aqueous dispersion liquid containing the lithium-containing oxide subjected to the mechanical milling treatment and the aqueous solution containing the lithium salt were mixed (the method 3 in the step 2B described above), and it is presumed that a larger amount of the lithium salt can be mixed, and as a result, the amount of Li incorporated into the solid electrolyte is increased. In addition, it was also found that the ion conductivity was further improved in Reference Examples 3, 4, and 5, in which LiFSI was used as the lithium salt. This is presumed to be because the increased Li includes Li having high mobility.

<Influence of Water in Solid Electrolyte>

The compacted powder body (pellet) (10 mmφ, 0.9 mmt (thickness)) of the solid electrolyte (I)-3 obtained in Reference Example 3 was vacuum-dried at 27° C. under a restraint of 60 MPa, and a pressure change and an ion conductivity with respect to a vacuum drying time were examined. The method of producing the compacted powder body and the evaluation of the ion conductivity are as described above, except that the In electrode is changed to the Ti electrode. The results are shown in Table 3.

	TABLE 3
	Vacuum		Ion
	drying time	Pressure	conductivity
	(min)	(Pa)	(27° C., S/cm)
	0	101325	4.8 × 10−3
	5	200	3.8 × 10−3
	20	20	3.3 × 10−3
	50	10	2.6 × 10−3
	1080	15	5.7 × 10−4

In the solid electrolyte (I)-3 of Reference Example 3, an absorption intensity derived from an O—H stretching peak was strongly observed in a wave number range of 3,000 to 3,500 cm⁻¹ in the infrared absorption spectrum, and thus it is considered that a large number of OH groups and water were present. In addition, it is presumed that water was present as free water and bound water. In the above, the pellets were dried under conditions that the pellets were considered to be volatilized from the free water by vacuum drying first, and the pellets were further dried under more severe drying conditions; and the ion conductivity in each stage was evaluated.

As shown in the above table, it is considered that the pressure was 200 Pa and the free water was in a vaporized state in a drying time of 5 minutes, but the ion conductivity was a high value of 3.8×10⁻³ S/cm, and even in a drying time of 1,080 minutes and a pressure of 15 Pa, the ion conductivity was 5.7×10⁻⁴ S/cm. This result indicates that bound water other than free water was present and contributed to the ion conductivity.

Reference Example 7: Production by Steps 1B to 3B and Method 3 Described Above

A dispersion liquid 9 in which the concentration of the fine substance of the lithium-containing oxide was 42% by mass was obtained in the same manner as in the preparation of the dispersion liquid 1 in Reference Example 3 described above.

Next, 7.12 g of LiTFSI (chemical formula: Li(F₃CSO₂)₂N) as a lithium salt was added to water such that a concentration was 87% by mass, and the mixture subjected to an ultrasonic treatment for 60 minutes to obtain a solution 10.

The obtained dispersion liquid 9 and solution 10 were mixed, and stirred and mixed with a magnetic stirrer for 60 minutes. Subsequently, the obtained dispersion liquid was vacuum-dried at 40° C. and 10 Pa for 15 hours to obtain a powdery solid electrolyte (I)-7. The obtained powder was allowed to stand in the air for a certain period of time, and various evaluations were performed in the air in the same manner as in Reference Example 1 using the solid electrolyte (I)-7. The results are summarized in the tables below.

Reference Example 8

A solid electrolyte (I)-8 was obtained in the same manner as in Reference Example 7, except that the content of water and LiTFSI in the obtained solid electrolyte (I) was changed to the amount shown in the table below; and various evaluations were performed in the air in the same manner as in Reference Example 1. The results are summarized in the tables below.

Reference Examples 9 to 13

Solid electrolytes (I)-9 to (I)-13 were obtained in the same manner as in Reference Example 7, except that LiTFSI was changed to LiFSI, and the content of water and LiFSI in the obtained solid electrolyte (I) was changed to the amount shown in the table below; and various evaluations were performed in the air in the same manner as in Reference Example 1. The results are summarized in the tables below. However, in Reference Example 13, the evaluation was performed in the air using the powder obtained by vacuum drying as soon as possible.

In the tables below, the columns of “Fine substance of lithium-containing oxide”, “Lithium salt”, and “Water” indicate relative molar ratios. For example, in Reference Example 7, the molar ratio of the lithium salt to the fine substance of the lithium-containing oxide was 1, and the molar ratio of the water to the fine substance of the lithium-containing oxide was 11. The above-described molar ratio was calculated by the following method.

Regarding the analysis of each of elements, quantitative analysis was performed by ICP-OES for lithium and boron or by combustion ion chromatography (combustion IC) for fluorine and sulfur, estimation was performed for N from the analytical mass of sulfur in consideration of the amount of each of atoms in the Li salt, the analytical masses of elements other than O were added together for O, and calculation was performed in terms of the difference from the total amount of the solid electrolyte. In Reference Examples 7 and 8, the carbon amount was estimated from the analytical mass of sulfur in consideration of the amount of each of atoms in the lithium salt. The molar ratio of the fine substance of the lithium-containing oxide in the solid electrolyte to the lithium salt was calculated from the molar ratio of an element (for example, B) which is present only in the fine substance of the lithium-containing oxide to an element which is present only in the lithium salt. In addition, the molar ratio of the fine substance of the lithium-containing oxide to the water was calculated by subtracting the molar ratio of O, contained in the fine substance of the lithium-containing oxide and the lithium salt, from the molar ratio of O in the solid electrolyte to calculate the molar amount of O derived from water, and using the obtained molar amount of O derived from water and the molar amount of the fine substance of the lithium-containing oxide.

TABLE 4
	Fine substance of the	Lithium
	lithium-containing oxide	salt	Water
Comparative	1	0	0
Reference
Example 2
Reference Example 7	1	1	11
Reference Example 8	1	1.2	11
Reference Example 9	1	0.01	4
Reference Example 10	1	0.03	4
Reference Example 11	1	0.5	11
Reference Example 12	1	0.7	11
Reference Example 13	1	1.0	6

In addition, the content (% by mass) of each component in the solid electrolyte (I) was calculated based on the molar amount and the molecular weight shown in Table 4. The results are shown in Table A.

TABLE A
	Fine substance of the	Lithium
	lithium-containing oxide	salt	Water
Comparative Reference	100	0	0
Example 2
Reference Example 7	26	44	30
Reference Example 8	24	48	28
Reference Example 9	70	1	29
Reference Example 10	69	2	29
Reference Example 11	37	20	43
Reference Example 12	34	26	40
Reference Example 13	36	40	24

TABLE 5
	Proportion of	Proportion	Maximum
	full-width at	of	absorption		Mass	Short	Long	X-ray	Ion
	half maximum	area	intensity	Coefficient of	reduction	distance	distance	diffraction	conductivity (S/cm)
	(%)	intensity	ratio	determination	rate (%)	G(r)	G(r)	characteristics	27° C.	60° C.
Comparative	46	C	B	0.9677	—	A	A	A	7.5 × 10−9	7.5 × 10−8
Reference
Example 2
Reference	—	B	A	—	—	—	—	A	7.4 × 10−4	—
Example 7
Reference	—	B	A	—	—	—	—	A	7.2 × 10−4	—
Example 8
Reference	33	B	A	0.9974	29.8	A	—	A	1.5 × 10−4	4.0 × 10−4
Example 9
Reference	—	A	A	0.9908	30	A	—	A	1.1 × 10−3	4.0 × 10−3
Example 10
Reference	—	A	A	—	—	A	—	A	4.1 × 10−3	—
Example 11
Reference	—	A	A	—	—	A	—	A	4.7 × 10−3	—
Example 12
Reference	—	A	A	—	—	A	—	A	3.0 × 10−3	—
Example 13

As shown in the above tables, the solid electrolyte of each of Reference Examples satisfied the composition specified in the claim 1 of the present application, had desired characteristics or physical properties, and exhibited excellent ion conductivity.

[Production Example 1] Production of Coating-Type Secondary Battery

<Preparation of Fine Substance of Lithium-Containing Oxide>

45 g of powdery Li₂B₄O₇ crystals (LBO powder) (manufactured by RARE METALLIC Co., Ltd.), 770 g of zirconia beads, and 3 mL of water were charged into a 500 mL zirconia pot, and the pot was sealed with a ring made of Teflon (registered trademark) and a lid made of zirconia. The mixture was subjected to a ball milling treatment using a planetary ball milling device (P-7, manufactured by FRITSCH) at 300 revolutions per minute (rpm) for 45 hours to pulverize the LBO powder, thereby obtaining a fine substance of a lithium-containing oxide.

<Preparation of Solid Electrolyte Slurry: Production of Solid Electrolyte (I) by Steps 1B to 3B and Method 1 Described Above>

10 g of the above-described fine substance of the lithium-containing oxide, 15 g of water, and 11 g of LiFSI were mixed in a beaker, and subjected to an ultrasonic treatment for 30 minutes using an ultrasonic cleaner to obtain a dispersion liquid. The dispersion liquid was further stirred with a magnetic stirrer for 30 minutes to obtain a solid electrolyte slurry 1.

The solid electrolyte slurry 1 was vacuum-dried at 40° C. and 20 Pa for 15 hours to obtain a powder. After storing the obtained powder in a desiccator (humidity: 5%) for several days and then analyzing in the air, it was confirmed that the powder had the above-described X-ray diffraction characteristics and was in an amorphous state. In addition, in a case where the ion conductivity was measured by the above-described method, the ion conductivity was 4.5×10⁻³ S/cm. In addition, the value of the ratio of the content of LiFSI to the content of the lithium-containing oxide was 1 in terms of a molar ratio; and the value of the ratio of the content of water to the content of the lithium-containing oxide was 9 in terms of a molar ratio. The element composition was Li=3, B=4, O=20, F=2, S=2, and N=1.

<Preparation of Positive Electrode Slurry>

5.0 g of a positive electrode active material LiCoO₂ (volume average particle size: 12 μm) and 4.8 g of a 6% by mass aqueous dispersion liquid of carbon nanotubes (CNT) (manufactured by KJ Special Paper Co., Ltd.) as a conductive auxiliary agent were added to 5.2 g of the above-described solid electrolyte slurry 1, and the mixture was stirred with a magnetic stirrer for 30 minutes to obtain a positive electrode slurry 1.

<Preparation of Negative Electrode Slurry>

5.0 g of a negative electrode active material TiNb₂O₇ (volume average particle size: 10 μm) and 9.8 g of a 6% by mass aqueous dispersion liquid of carbon nanotubes (CNT) (manufactured by KJ Special Paper Co., Ltd.) as a conductive auxiliary agent were added to 7.6 g of the above-described solid electrolyte slurry 1, and the mixture was stirred with a magnetic stirrer for 30 minutes to obtain a negative electrode slurry 1.

<Preparation of Positive Electrode-Side Laminate [Solid Electrolyte Layer/Positive Electrode Active Material Layer/Al Collector Layer]>

The above-described positive electrode slurry 1 was applied onto an A4-sized Al foil having a thickness of 50 μm using a desktop coating machine at an applicator gap of 100 μm and an application speed of 30 mm/s. After being left to stand at room temperature for 1 hour, the above-described solid electrolyte slurry 1 was applied onto a positive electrode slurry coating film in a multilayer manner using a desktop coating machine at an applicator gap of 200 μm and a coating rate of 90 mm/s. The multilayer coating film was stored in a desiccator having a relative humidity of 5% or less for 12 hours and dried, and punched with a hand punch to have a diameter of 10 mm, thereby obtaining a positive electrode-side laminate (solid electrolyte layer/positive electrode active material layer/Al collector layer). A thickness of the solid electrolyte layer was approximately 60 μm.

<Preparation of Negative Electrode-Side Laminate [Solid Electrolyte Layer/Negative Electrode Active Material Layer/Al Collector Layer]>

The above-described negative electrode slurry 1 was applied onto an A4-sized Al foil having a thickness of 50 μm using a desktop coating machine at an applicator gap of 200 μm and an application speed of 30 mm/s. After being left to stand at room temperature for 1 hour, the above-described solid electrolyte slurry 1 was applied onto a negative electrode slurry coating film in a multilayer manner using a desktop coating machine at an applicator gap of 300 μm and a coating rate of 90 mm/s. The multilayer coating film was stored in a desiccator having a relative humidity of 5% or less for 12 hours and dried, and punched with a hand punch to have a diameter of 10 mm, thereby obtaining a negative electrode-side laminate (solid electrolyte layer/negative electrode active material layer/Al collector layer). A thickness of the solid electrolyte layer was approximately 60 μm.

<Production of Coating-Type Secondary Battery>

The negative electrode-side laminate obtained above was placed on a 10 mm-diameter SUS base of an all-solid-state battery evaluation cell (product name: KP-SolidCell) manufactured by Hohsen Corp. with the solid electrolyte layer side facing upward, and the positive electrode-side laminate obtained above was further placed thereon with the solid electrolyte layer side facing downward.

Subsequently, a tube made of Teflon (registered trademark) (hereinafter, referred to as a Teflon tube) having an inner diameter of 10.2 mm was fitted from the upper side (on a side of the positive electrode-side laminate) of a cell A formed by laminating the positive electrode-side laminate/the negative electrode-side laminate in this order, a polished Ti plate having a diameter of 10 mm and a thickness of 2 mm was put in from a hole in an upper part of the Teflon tube and placed on the positive electrode laminate, and a Ti rod having a diameter of 10 mm and a height of 2 cm was put in and placed on the Ti plate.

Subsequently, the upper housing of the KP-SolidCell was fitted and sealed using a double O-ring, a 4-point bolt, and a butterfly nut. The cell A was restrained from above and below by a restraining pressure applying mechanism provided on the upper part of the KP-SolidCell at a torque of 5 Nm (corresponding to 30 MPa).

Subsequently, the KP-SolidCell was temporarily opened to take out the cell A, the excess liquid component which had bleed out due to the application of the restraining pressure was wiped off, the cell A was set in the KP-SolidCell again in the same manner as described above, and the restraining pressure was applied at a torque of 5 Nm (corresponding to 30 MPa).

Thereafter, the upper lid was opened, and the cell A was subjected to freeze vacuum drying for 2 hours to sufficiently remove moisture inside the cell A. After taking out the KP-SolidCell from the vacuum dryer, the upper lid was closed and sealed through a double O-ring. The cell was left to stand at room temperature for 40 hours to produce a coating-type secondary battery A.

A coating-type secondary battery B was produced in the same manner as in the production of the coating-type secondary battery A described above, except that, in the production of the coating-type secondary battery A described above, a 50 μm-thick A4-sized Ti foil was used instead of the 50 μm-thick A4-sized Al foil as the collector layer in the positive electrode, and a 50 μm-thick A4-sized Cu foil was used instead of the 50 μm-thick A4-sized Al foil as the collector layer in the negative electrode.

In the coating-type secondary batteries A and B, the thickness of the positive electrode active material layer was 80 μm, the thickness of the solid electrolyte layer was 120 μm, and the thickness of the negative electrode active material layer was 100 μm.

[Production Example 2] Production of Compacted Powder-Type Secondary Battery

<Preparation of Solid Electrolyte Powder 1: Production of Solid Electrolyte (I) by Steps 1B to 3B and Method 1 Described Above>

10 g of fine substance of the lithium-containing oxide prepared in Production Example 1 described above, 15 g of water, and 11 g of LiFSI were mixed in a beaker, subjected to an ultrasonic treatment (dispersion) for 30 minutes using an ultrasonic cleaner, and further stirred and dispersed for 30 minutes with a magnetic stirrer to obtain a solid electrolyte slurry. The obtained slurry was freeze-dried at 40° C. and 10 Pa for 12 hours to obtain a solid electrolyte powder 1.

<Preparation of Positive Electrode Mixture Powder 1>

100 mg of the above-described solid electrolyte powder 1, 150 mg of a positive electrode active material LiCoO₂ (volume average particle size: 12 μm), and 3 mg of a conductive auxiliary agent carbon black (manufactured by Denka Company Limited) were mixed in a mortar to obtain a positive electrode mixture powder 1.

<Preparation of Negative Electrode Mixture Powder 1>

60 mg of the above-described solid electrolyte powder 1, 120 mg of a negative electrode active material cLTO (LTO having a carbon coating layer; volume average particle size: 10 μm), and 3 mg of a conductive auxiliary agent carbon black (manufactured by Denka Company Limited) were mixed in a mortar to obtain a negative electrode mixture powder 1.

<Production of Compacted Powder Molded Body>

An SUS punch (short) having a diameter of 10 mm was inserted into a hole in the lower part of an SUS tube for powder compaction molding (inner diameter: 10 mm), and the above-described solid electrolyte powder 1 was put in from a hole in the upper part of the SUS tube and leveled. An SUS punch (long) was inserted from the upper hole and then pressurized at 50 MPa for 10 seconds using a hydraulic press, and the pressure was released to pull out the SUS punch (long) from the SUS tube.

Subsequently, the negative electrode mixture powder 1 was put into the upper hole of the SUS tube and leveled on the compacted powder layer of the solid electrolyte powder 1. An SUS punch (long) was inserted from the upper hole and then pressurized at 50 MPa for 10 seconds using a hydraulic press, and the pressure was released. Thereafter, the upper and lower sides were reversed from a state in which the SUS punch (long)/SUS pipe/SUS punch (short) was on the upper side and the SUS punch (short) was on the lower side, so that the SUS punch (short) was on the upper side, and then the SUS punch (short) was pulled out from the SUS pipe.

The positive electrode mixture powder 1 was put into the upper hole of the SUS tube and leveled on the compacted powder layer of the solid electrolyte powder 1. An SUS punch (short) was inserted from the upper hole and then pressurized at 200 MPa for 10 seconds using a hydraulic press, and the pressure was released to pull out the SUS punch (long) from the SUS tube. Thereafter, using a punching die, a compacted powder molded body in which the compacted powder layer of the negative electrode mixture powder 1/the compacted powder layer of the solid electrolyte powder 1/the compacted powder layer of the positive electrode mixture powder 1 were laminated in this order was taken out, and the excess liquid component which had bleed out was wiped off.

<Production of Compacted Powder-Type Secondary Battery>

A 50 μm-thick Al foil (negative electrode-side collector layer) punched out to a diameter of 10 mm was placed on a 10 mm-diameter SUS base of an all-solid-state battery evaluation cell (product name: KP-SolidCell) manufactured by Hohsen Corp., and the above-described compacted powder molded body was placed thereon with the negative electrode side facing downward. A Teflon tube having an inner diameter of 10.2 mm was fitted, a 50 μm-thick Al foil (positive electrode-side collector layer) punched out to a diameter of 10 mm was placed from a hole in the upper part of the Teflon tube, a polished Ti plate having a diameter of 10 mm and a thickness of 2 mm was placed thereon, and a Ti rod having a diameter of 10 mm and a height of 2 cm was further placed thereon and placed on the Ti plate.

Subsequently, the upper housing of the KP-SolidCell was fitted and sealed using a double O-ring, a 4-point bolt, and a butterfly nut. A cell B was restrained from above and below by a restraining pressure applying mechanism provided on the upper part of the KP-SolidCell at a torque of 9 Nm (corresponding to 60 MPa). Here, the cell B means a cell in which the negative electrode-side collector layer, the compacted powder molded body, and the positive electrode-side collector layer were laminated in this order.

Subsequently, the KP-SolidCell was temporarily opened to take out the cell B, the excess liquid component which had bleed out due to the application of the restraining pressure was wiped off, the cell B was set in the KP-SolidCell again in the same manner as described above, and the restraining pressure was applied at a torque of 9 Nm (corresponding to 60 MPa).

Thereafter, the upper lid was opened, and the cell B was subjected to freeze vacuum drying for 2 hours to sufficiently remove moisture inside the cell A. After taking out the KP-SolidCell from the vacuum dryer, the upper lid was closed and sealed through a double O-ring. The cell was left to stand at room temperature for 40 hours to produce a compacted powder-type secondary battery C. In the compacted powder-type secondary battery C, the thickness of the positive electrode active material layer was 100 μm, the thickness of the solid electrolyte layer was 200 μm, and the thickness of the negative electrode active material layer was 100 μm.

The configurations of the secondary batteries and evaluation results of a charging and discharging test are summarized in Table 6.

(Charging and Discharging Test)

The coating-type secondary battery obtained as described above was applied to a restraining pressure (30 MPa), and under a temperature condition of 27° C., charging and discharging were repeatedly performed under the following conditions using 580-NOHFR (trade name) manufactured by TOYO TECHNIKA CO., LTD. as a charging and discharging device. In addition, the compacted powder-type secondary battery obtained as described above was repeatedly charged and discharged under the following conditions in the same manner as the coating-type secondary battery, except that the restraining pressure was changed to 60 MPa.

The charging was performed at a constant current value Is until the desired battery voltage reached 2.8 V, and after reaching 2.8 V, the voltage was made constant (2.8 V) and the charging was performed until the current value reached 2.4 C.

After the charging, the circuit was opened and left to stand for 10 minutes, and then the battery was discharged at a constant current value I_β until the battery voltage reached 1.5 V.

The charging and discharging up to this point were defined as one cycle.

After the discharging, the circuit was opened and left to stand for 10 minutes and then next charging was performed, and the charging and discharging were repeated under the same conditions.

In the above-described charging and discharging, the current value Is was set to 0.2 C in the first cycle of charging and discharging as initialization of the battery, and was set to 3 C in subsequent charging and discharging, and a charging and discharging cycle test was performed.

In addition, a discharge capacity retention rate (%) was calculated according to the following expression, and evaluated based on the following evaluation standard.

Discharge capacity retention rate (%)=(Discharge capacity after 50 cycles of charging and discharging at 3 C/Discharge capacity after 10 cycles of charging and discharging at 3 C)×100

—Evaluation Standard—

• • A: discharge capacity retention rate was 70% or more.
  • B: discharge capacity retention rate was 40% or more and less than 70%.
  • C: discharge capacity retention rate was less than 40%.

TABLE 6
			Discharge	Discharge
			capacity	capacity
			after 10	retention
			cycles of	rate after
			charging	50 cycles
		Coating	and	of charging
		type or	discharging	and
	Collecting foil	compacted	at 3C	discharging
Battery	Positive	Negative	powder	(mAh/g)	at 3C
No.	electrode	electrode	type	Evaluation	Evaluation
A	Al	Al	Coating	110	A
			type
B	Ti	Cu		60	B
C	Al	Al	Compacted	60	A
			powder
			type

From Table 6, it was found that the secondary battery according to the embodiment of the present invention, which included the solid electrolyte layer containing the solid electrolyte (I), exhibited excellent charging and discharging cycle characteristics and operated as a secondary battery.

As described above, in the secondary battery according to the embodiment of the present invention, even in a case where an oxide-based solid electrolyte was used, the bonding property between particles were excellent, and a collector layer containing a metal which is difficult to use under conditions for performing high-temperature sintering could be used. In addition, with the manufacturing method of the secondary battery according to the embodiment of the present invention, even in a case where an oxide-based solid electrolyte was used, the bonding property between particles were excellent, and it was possible to manufacture a secondary battery using a collector layer containing a metal which is difficult to use under conditions for performing high-temperature sintering in an atmosphere containing oxygen gas.

The present invention has been described with the embodiments thereof, any details of the description of the present invention are not limited unless described otherwise, and it is obvious that the present invention is widely construed without departing from the gist and scope of the present invention described in the accompanying claims.

EXPLANATION OF REFERENCES

• • 1: negative electrode collector layer
  • 2: negative electrode active material layer
  • 3: solid electrolyte layer
  • 4: positive electrode active material layer
  • 5: positive electrode collector layer
  • 6: operation portion
  • 10: all-solid-state lithium ion secondary battery

Claims

1. An all-solid-state lithium ion secondary battery comprising: at least one or more laminates in which a positive electrode layer, a solid electrolyte layer, and a negative electrode layer are arranged in this order,wherein at least one of the positive electrode layer or the negative electrode layer includes a collector layer,at least one collector layer is a layer having, as a constitutional material, a metal melted at 670° C. under normal pressure or a layer having the metal in a coating layer, andthe solid electrolyte layer contains an amorphous solid electrolyte which contains a lithium-containing oxide containing Li, B, and O, water, and a lithium salt, and in the amorphous solid electrolyte, a value of a ratio of a content of the lithium salt to a content of the lithium-containing oxide is 0.001 to 1.5 in terms of a molar ratio, and a value of a ratio of a content of the water to the content of the lithium-containing oxide is 1 to 12 in terms of a molar ratio.

2. The all-solid-state lithium ion secondary battery according to claim 1, wherein the metal melted at 670° C. under normal pressure is Al or an Al alloy.

3. The all-solid-state lithium ion secondary battery according to claim 1, wherein the lithium-containing oxide includes Li2+xB4+yO7+z,where −0.3<x<0.3, −0.3<y<0.3, and −0.3<z<0.3.

4. A manufacturing method of an all-solid-state lithium ion secondary battery including at least one or more of the laminates in which a positive electrode layer, a solid electrolyte layer, and a negative electrode layer are arranged in this order, the manufacturing method comprising: manufacturing the laminate of the positive electrode layer, the solid electrolyte layer, and the negative electrode layer at 300° C. or lower in an atmosphere containing oxygen gas,wherein at least one of the positive electrode layer or the negative electrode layer includes a collector layer,at least one collector layer is a layer having Cu as a constitutional material or a layer having Cu in a coating layer, andthe solid electrolyte layer contains an amorphous solid electrolyte which contains a lithium-containing oxide containing Li, B, and O, water, and a lithium salt, and in the amorphous solid electrolyte, a value of a ratio of a content of the lithium salt to a content of the lithium-containing oxide is 0.001 to 1.5 in terms of a molar ratio, and a value of a ratio of a content of the water to the content of the lithium-containing oxide is 1 to 12 in terms of a molar ratio.