JP5197918B2 - All-solid lithium ion secondary battery and solid electrolyte - Google Patents

Description

  The present invention relates to a solid electrolyte suitable mainly for a lithium ion secondary battery and a lithium ion secondary battery equipped with the solid electrolyte.

Conventionally, as an electrolyte in a lithium ion secondary battery, an electrolyte obtained by impregnating a microporous membrane called a separator with a nonaqueous electrolytic solution has been used, but in recent years, such a liquid is mainly used as an electrolyte. Instead, lithium ion secondary batteries (polymer batteries) using polymer electrolytes composed of polymers have been attracting attention.
This polymer battery uses a gel electrolyte in which a liquid electrolyte is impregnated in a polymer, and since the electrolyte is retained in the polymer, it is difficult to leak, thus improving battery safety. In addition, there are advantages such as freedom in the shape of the battery.

  Here, since such a polymer electrolyte has lower conductivity of lithium ions than the electrolytic solution alone, the thickness of the polymer electrolyte has been reduced. However, when the polymer electrolyte is made thin in this way, its mechanical strength is lowered, and this polymer electrolyte is destroyed at the time of producing a battery, so that there is a problem that the positive electrode and the negative electrode are easily short-circuited.

  Therefore, conventionally, as disclosed in Patent Document 1, it has been proposed that an inorganic oxide such as alumina is added to an electrolyte to form a solid electrolyte to improve mechanical strength. In addition to alumina, inorganic oxides such as silica and lithium aluminate have been proposed.

  However, when an inorganic oxide such as alumina is added to the electrolyte, there is a problem that the conductivity of lithium ions in the solid electrolyte is greatly reduced. In addition, if charging / discharging is repeated in a lithium secondary battery equipped with this solid electrolyte, the electrolyte reacts with the inorganic oxide, and the charge / discharge cycle characteristics of the lithium secondary battery are greatly reduced. was there.

In addition, in a lithium ion secondary battery including a polymer solid electrolyte, thermal expansion and contraction due to a temperature change and a rapid change in ionic conductivity are unavoidable due to polymer characteristics. Therefore, the lithium ion secondary battery containing such a polymer solid electrolyte has a low heat-resistant temperature and cannot be used in a wide temperature range.
JP-A-6-140052

  This invention is an all-solid-state lithium ion secondary battery that has a high heat resistance, can be used in a wide temperature range, has a high battery capacity, good charge / discharge cycle characteristics, and is stable over the long term. It is an object of the present invention to provide a solid electrolyte or an all solid lithium secondary battery that can be used.

  In order to solve the above-mentioned problems, the present inventor does not include an electrolyte in the solid electrolyte from the viewpoint of battery safety, and further does not include an organic substance in the solid electrolyte from the viewpoint of improving the heat-resistant temperature. I found it important. Furthermore, as a result of intensive studies and research on the configuration of solid electrolytes and lithium ion secondary batteries having excellent practicality under such conditions, lithium ion conductive crystals of a specific composition were found in the solid electrolytes. An inorganic substance containing lithium ion conductive glass ceramics, or an inorganic substance containing a lithium ion conductive crystal having a specific composition also in the positive electrode and / or negative electrode of a secondary battery using such a solid electrolyte, In particular, by including lithium ion conductive glass ceramics, it has higher heat resistance, can be used in a wide temperature range, and has a high battery capacity and charge / discharge cycle characteristics compared to conventional all solid electrolyte batteries. Found that a solid electrolyte or an all-solid-state lithium secondary battery that can be used stably for a long period of time is obtained. Those were.

  That is, the first configuration of the present invention is a solid electrolyte characterized in that it contains an inorganic substance containing a lithium ion conductive crystal and does not contain an organic substance or an electrolytic solution.

  According to a second configuration of the present invention, the solid electrolyte of the first configuration of the present invention is characterized in that the inorganic substance containing a lithium ion conductive crystal does not contain vacancies or crystal grain boundaries that inhibit ion conduction. It is.

  Here, in this specification, the vacancy or grain boundary that inhibits ion conduction refers to the conductivity of the entire inorganic substance including lithium ion conductive crystals, and the conductivity of the lithium ion conductive crystal itself in the inorganic substance. On the other hand, it refers to ionic conductivity inhibiting factors such as vacancies and grain boundaries that are reduced to 1/10 or less.

  A third configuration of the present invention is the solid electrolyte according to the first or second configuration of the present invention, wherein the inorganic substance containing a lithium ion conductive crystal is a lithium ion conductive glass ceramic.

  According to a fourth aspect of the present invention, there is provided an inorganic substance powder or lithium ion conductive glass ceramic powder containing lithium ion conductive crystals, and an inorganic compound containing Li. To 3. A solid electrolyte having any one of the constitutions 3 to 3.

In the fifth configuration of the present invention, the inorganic substance powder or lithium ion conductive glass ceramic powder containing lithium ion conductive crystals has an ion conductivity of 10 ⁻⁴ Scm ⁻¹ or more, and an average particle size Is 9 μm or less, and is contained in the solid electrolyte in an amount of 50 to 95% by mass.

  A sixth configuration of the present invention is the solid electrolyte of the third configuration of the present invention, characterized in that the lithium ion conductive glass ceramic is in a thin plate shape.

  The seventh configuration of the present invention is the solid electrolyte of the sixth configuration of the present invention, wherein the lithium ion conductive glass ceramic has a thickness of 15 μm to 200 μm.

An eighth configuration of the present invention is the solid electrolyte according to any one of the first to seventh configurations of the present invention, wherein the ionic conductivity is 10 ⁻⁵ Scm ⁻¹ or more.

According to a ninth configuration of the present invention, an inorganic substance containing lithium ion conductive crystals or a lithium ion conductive glass ceramic has a main crystal phase of Li _{1 + x + y} Al _x Ti _2-x Si _y P _3-y O ₁₂ , The solid electrolyte according to any one of the first to eighth aspects of the present invention, wherein 0 ≦ x ≦ 1 and 0 ≦ y ≦ 1.

In the tenth configuration of the present invention, an inorganic substance containing lithium ion conductive crystals or lithium ion conductive glass ceramics is expressed in mol%.
Li ₂ O: 12~18%, and _{Al 2 O 3 + Ga 2 O} 3: 5~10%, and _{TiO 2 + GeO 2: 35~45%} , and SiO _2: 1~10%, and P ₂ O _5: 30-40%
The solid electrolyte according to any one of the first to ninth aspects of the present invention is characterized by containing the following components.

In an eleventh configuration of the present invention, the inorganic substance containing lithium ion conductive crystals or the lithium ion conductive glass ceramic is represented by mass%,
Li ₂ O: 3~10%, and _{Al 2 O 3 + Ga 2 O} 3: 5~20%, and _{TiO 2 + GeO 2: 25~40%} , and SiO _2: 0.5~8%, and P ₂ O ₅ : 40-55%
The solid electrolyte according to any one of the first to ninth aspects of the present invention is characterized by containing the following components.

  A twelfth configuration of the present invention is a lithium ion secondary battery comprising the solid electrolyte according to any one of the first to eleventh configurations of the present invention.

  A thirteenth configuration of the present invention is the lithium ion secondary battery according to the twelfth configuration of the present invention, wherein the positive electrode and / or the negative electrode contains an inorganic substance containing lithium ion conductive crystals.

  According to a fourteenth aspect of the present invention, the inorganic substance containing lithium ion conductive crystals contained in the positive electrode and / or the negative electrode does not contain vacancies or crystal grain boundaries that inhibit ion conduction. This is a lithium ion secondary battery having the thirteenth configuration.

  According to a fifteenth aspect of the present invention, in any one of the thirteenth and fourteenth aspects of the present invention, the inorganic substance containing a lithium ion conductive crystal contained in the positive electrode and / or the negative electrode is a lithium ion conductive glass ceramic. This is a lithium ion secondary battery having such a configuration.

  According to a sixteenth configuration of the present invention, the average particle diameter of the inorganic substance or lithium ion conductive glass ceramic containing lithium ion conductive crystals contained in the positive electrode and / or the negative electrode is inorganic containing the lithium ion conductive crystals. The lithium ion secondary material according to any one of the thirteenth to fifteenth aspects of the present invention, characterized in that the average particle diameter of the active material of the positive electrode and / or negative electrode containing the material or lithium ion conductive glass ceramics is 1/5 or less. Next battery.

  According to a seventeenth configuration of the present invention, the content of the inorganic material or lithium ion conductive glass ceramic containing a lithium ion conductive crystal contained in the positive electrode and / or the negative electrode depends on the positive electrode and / or negative electrode active material contained therein. The lithium ion secondary battery according to any one of the thirteenth to sixteenth aspects of the present invention is characterized by being 2 to 35% by mass.

According to an eighteenth configuration of the present invention, an inorganic substance or lithium ion conductive glass ceramic containing a lithium ion conductive crystal contained in a positive electrode and / or a negative electrode is expressed in mol%,
Li ₂ O: 12~18%, and _{Al 2 O 3 + Ga 2 O} 3: 5~10%, and _{TiO 2 + GeO 2: 35~45%} , and SiO _2: 1~10%, and P ₂ O _5: 30-40%
The lithium ion secondary battery according to any one of the thirteenth to seventeenth aspects of the present invention is characterized by containing the following components.

According to a nineteenth configuration of the present invention, an inorganic substance or lithium ion conductive glass ceramic containing a lithium ion conductive crystal contained in a positive electrode and / or a negative electrode is represented by mass%,
Li ₂ O: 3~10%, and _{Al 2 O 3 + Ga 2 O} 3: 5~20%, and _{TiO 2 + GeO 2: 25~40%} , and SiO _2: 0.5~8%, and P ₂ O ₅ : 40-55%
The lithium ion secondary battery according to any one of the thirteenth to seventeenth aspects of the present invention is characterized by containing the following components.

In a twentieth configuration of the present invention, an inorganic substance or lithium ion conductive glass ceramic containing a lithium ion conductive crystal contained in a positive electrode and / or a negative electrode has a main crystal phase of Li _{1 + x + y} Al _x Ti _2−x Si _y. The lithium ion secondary battery according to any one of the thirteenth to nineteenth aspects of the present invention, wherein P _3−y O ₁₂ (0 ≦ x ≦ 1, 0 ≦ y ≦ 1).

  According to a twenty-first configuration of the present invention, the positive electrode and / or the negative electrode contains the same inorganic substance or glass ceramic as the inorganic substance containing lithium ion conductive crystals or lithium ion conductive glass ceramic contained in the solid electrolyte. The lithium ion secondary battery according to any one of the thirteenth to seventeenth aspects of the present invention is characterized.

The configuration of the present invention will be described in detail.
The solid electrolyte of the present invention does not contain organic matter and electrolyte. By setting it as such a structure, the danger by the electrolyte leakage can be avoided. In addition, thermal expansion / contraction due to temperature change is small, there is no sudden change in conductivity, and the heat-resistant temperature becomes high, so that it can be used well in a wide temperature range.

  Therefore, the lithium ion conductive substance contained in the solid electrolyte of the present invention is preferably an inorganic substance, and a material having almost no vacancies between crystal grains or in the crystal is obtained, and exhibits good ionic conductivity. Therefore, this inorganic substance is particularly preferably glass ceramics.

  Here, in the present invention, not containing organic substances and electrolyte means that it is not intentionally contained, and when it is mixed as an impurity or contained in a manufacturing process, it is removed in a subsequent process. In some cases, a small amount remains unintentionally.

In this specification, the glass ceramic is a material obtained by precipitating a crystal phase in a glass phase by heat-treating glass, and means a material composed of an amorphous solid and a crystal. Glass ceramic is a material in which the entire glass phase is phase-transformed into a crystal phase if there are almost no vacancies between crystal grains or in the crystal, that is, the crystal amount (crystallinity) in the material is 100% by mass. Also included. Generally speaking, ceramics and sintered bodies are inevitably present in the production process between crystal grains and in the presence of vacancies and crystal grain boundaries in crystals, and can be distinguished from glass ceramics.
In particular, with regard to ionic conduction, in the case of ceramics, due to the presence of vacancies and crystal grain boundaries, the value is considerably lower than the conductivity of the crystal grains themselves. Glass ceramics can suppress a decrease in conductivity between crystals by controlling the crystallization process, and can maintain the same conductivity as crystal grains.

  As described above, glass ceramics have better ionic conductivity than ceramics and sintered bodies, which are generally referred to, because there are no vacancies or grain boundaries that impede ionic conduction between the crystal grains or in the crystals. Degrees.

  When the solid electrolyte containing an inorganic substance having lithium ion conductive crystals or a lithium ion conductive glass ceramic of the present invention is used as a battery, a thin battery has a shorter lithium ion transfer distance, and thus a high output battery can be obtained. In addition, since a large electrode area per unit volume can be secured, a high-capacity battery can be obtained. Therefore, the thickness of the solid electrolyte containing lithium ion conductive glass ceramic powder used as the solid electrolyte is preferably 60 μm or less, more preferably 50 μm or less, and most preferably 40 μm or less. When the solid electrolyte is a glass ceramic thin plate, the thickness of the thin plate becomes the thickness of the solid electrolyte, and the thickness of the solid electrolyte is preferably 200 μm or less, more preferably 150 μm or less, and most preferably 100 μm or less.

  However, if the thickness is excessively thin, the mechanical strength of the solid electrolyte is lowered, and it becomes difficult to handle only the solid electrolyte during transportation, battery production, etc., which is not preferable in actual industrial battery production. Therefore, from the above viewpoint, the thickness of the solid electrolyte is preferably 15 μm or more, more preferably 20 μm or more, and most preferably 25 μm or more.

The mobility of lithium ions during charging and discharging of a lithium secondary battery depends on the lithium ion conductivity and the lithium ion transport number of the electrolyte. Therefore, the ionic conductivity of the solid electrolyte and the inorganic substance having lithium ion conductive crystals or the lithium ion conductive glass ceramic contained in the positive electrode and / or the negative electrode is 1 × 10 ⁻⁴ S · cm ⁻¹ or more. Preferably, it is 5 × 10 ⁻⁴ S · cm ⁻¹ or more, more preferably 1 × 10 ⁻³ S · cm ⁻¹ or more, and has a lithium ion conductive crystal. The ionic conductivity of the solid electrolyte containing an inorganic substance or lithium ion conductive glass ceramics is preferably 1 × 10 ⁻⁵ S · cm ⁻¹ or more, and preferably 5 × 10 ⁻⁵ S · cm ⁻¹ or more. Is more preferable, and 1 × 10 ⁻⁴ S · cm ⁻¹ or more is most preferable.

  On the other hand, the inorganic substance powder having a lithium ion conductive crystal having high ion conductivity or the lithium ion conductive glass ceramic powder to be contained in the solid electrolyte of the present invention is an inorganic substance having a lithium ion conductive crystal. A material or lithium ion conductive glass ceramic pulverized is used. This powder is preferably dispersed uniformly in the solid electrolyte from the viewpoint of ion conductivity and mechanical strength of the solid electrolyte. In order to improve dispersibility and to obtain a desired solid electrolyte thickness, the average particle size of the powder is preferably 9 μm or less, more preferably 6 μm or less, and most preferably 3 μm or less.

The lithium ion conductive glass ceramics contained in the solid electrolyte of the present invention or the lithium ion conductive glass ceramics contained in the positive electrode and / or negative electrode of the lithium ion secondary battery of the present invention has a base glass of Li ₂ O— Al ₂ O ₃ —TiO ₂ —SiO ₂ —P ₂ O ₅ -based composition, this glass is crystallized by heat treatment, and the main crystal phase at that time is Li _{1 + x + y} Al _x Ti _2−x Si _y P ₃ a glass ceramics is characterized by a _{-y O 12 (0 ≦ x ≦} 1,0 ≦ y ≦ 1). From the viewpoint of good ionic conductivity, more preferably 0 ≦ x ≦ 0.4, 0 <y ≦ 0.6, most preferably 0.1 ≦ x ≦ 0.3, 0.1 <y ≦ 0.4. It is.

An inorganic substance having a lithium ion conductive crystal contained in the solid electrolyte of the present invention or an inorganic substance having a lithium ion conductive crystal contained in the positive electrode and / or negative electrode of the lithium ion secondary battery of the present invention is the main crystalline phase is characterized by a _{Li 1 + x + y Al x} Ti 2-x Si y P 3-y O 12 (0 ≦ x ≦ 1,0 ≦ y ≦ 1). From the viewpoint of good ionic conductivity, more preferably 0 ≦ x ≦ 0.4, 0 <y ≦ 0.6, most preferably 0.1 ≦ x ≦ 0.3, 0.1 <y ≦ 0.4. It is.

  The composition ratio and the effect expressed by mol% of each component constituting the lithium ion conductive glass ceramic will be specifically described.

The Li ₂ O component is an essential component for providing Li ⁺ ion carriers and providing lithium ion conductivity. In order to obtain good conductivity, the lower limit of the content is preferably 12%, more preferably 13%, and most preferably 14%. The upper limit is preferably 18%, more preferably 17%, and most preferably 16%.

The Al ₂ O ₃ component can enhance the thermal stability of the mother glass, and at the same time, Al ³⁺ ions are dissolved in the crystal phase, and are effective in improving lithium ion conductivity. In order to obtain this effect, the lower limit of the content is preferably 5%, more preferably 5.5%, and most preferably 6%. However, if the content exceeds 10%, the thermal stability of the glass is deteriorated and the conductivity of the glass ceramic is also lowered. Therefore, the upper limit of the content is preferably 10%. In addition, the upper limit of more preferable content is 9.5%, and the upper limit of the most preferable content is 9%.

The TiO ₂ component and the Ge ₂ O ₃ component contribute to the formation of glass and are also constituents of the crystal phase, and both can be continuously substituted in the glass and the crystal. In order to vitrify, at least one of them must be included. In order to obtain a high conductivity by precipitating the crystal phase as a main phase from the glass, the lower limit of the total content of both components is 35%. Preferably, it is 36%, more preferably 37%. Further, the upper limit of the total content of both components is preferably 45%, more preferably 43%, and most preferably 42%.

The SiO ₂ component can improve the meltability and thermal stability of the mother glass, and at the same time, Si ⁴⁺ ions are dissolved in the crystal phase, contributing to an improvement in lithium ion conductivity. In order to sufficiently obtain this effect, the lower limit of the content is preferably 1%, more preferably 2%, and most preferably 3%. However, if the content exceeds 10%, the conductivity will be lowered. Therefore, the upper limit of the content is preferably 10%, more preferably 8%, and most preferably 7%. preferable.

The P ₂ O ₅ component is an essential component for the formation of glass, and is also a constituent component of the crystal phase. If the content is less than 30%, vitrification becomes difficult, so the lower limit of the content is preferably 30%, more preferably 32%, and most preferably 33%. Further, if the content exceeds 40%, the crystal phase hardly precipitates from the glass and it becomes difficult to obtain desired characteristics. Therefore, the upper limit of the content is preferably 40%, more preferably 39%. , 38% is most preferable.

  The composition ratio of each of the above-described components expressed by mass% for obtaining the same effect as that obtained by the composition ratio expressed by mol% is as follows.

The lower limit of the content of the Li ₂ O component is preferably 3% by mass, more preferably 4% by mass, and most preferably 5% by mass. The upper limit is preferably 10% by mass, more preferably 9% by mass, and most preferably 8% by mass.

The lower limit of the content of the Al ₂ O ₃ component is preferably 5% by mass, more preferably 6% by mass, and most preferably 7% by mass. The upper limit of the content is preferably 20% by mass. A more preferable upper limit of the content is 19% by mass, and a most preferable upper limit of the content is 18% by mass.

The lower limit of the total content of both components of the TiO ₂ and GeO ₂ components is preferably 25% by mass, more preferably 26% by mass, and most preferably 27% by mass. The upper limit of the total content of both components is preferably 40% by mass, more preferably 39% by mass, and most preferably 38% by mass.

The lower limit of the content of the SiO ₂ component is preferably 0.5% by mass, more preferably 1% by mass, and most preferably 2% by mass. The upper limit of the content is preferably 8% by mass, more preferably 7% by mass, and most preferably 6% by mass.

The lower limit of the content of the P ₂ O ₅ component is preferably 40% by mass, more preferably 41% by mass, and most preferably 42% by mass. The upper limit of the content is preferably 55% by mass, more preferably 54% by mass, and most preferably 53% by mass.

  In the case of the above-mentioned composition, glass can be easily obtained by casting molten glass, and glass ceramics having the crystal phase obtained by heat-treating this glass have high lithium ion conductivity.

In addition to the composition of the well, as long as the glass-ceramics having a crystal structure similar to, it is also possible to replace part or all of the _Al 2 _{O 3} and _{Ga 2 O} 3, TiO 2 into GeO _2. Furthermore, in the production of glass ceramics, in order to lower the melting point or increase the stability of the glass, it is also possible to add a small amount of other raw materials within a range where the ion conductivity is not lowered.

When the solid electrolyte contains an inorganic substance or glass ceramic powder containing lithium ion conductive crystals, it is preferable to contain an inorganic compound containing Li simultaneously. This is because an inorganic compound containing Li serves as a binder and serves to bind inorganic particles or glass ceramic particles containing lithium ion conductive crystals.
Examples of the inorganic compound containing Li include Li ₃ PO ₄ , LiPO ₃ , LiI, LiN, Li ₂ O, Li ₂ O ₂ , and LiF.
In particular, these inorganic compounds containing Li are softened or melted by adjusting the sintering temperature / atmosphere when they are mixed and sintered with an inorganic substance containing lithium ion conductive crystals or glass ceramics. It is possible. The softened or melted inorganic compound containing Li flows into the gaps between the glass ceramic particles, and can firmly bond the inorganic substance or glass ceramic containing lithium ion conductive crystals.

  Here, when an inorganic substance containing lithium ion conductive crystals having high ion conductivity or lithium ion conductive glass ceramic powder is contained in the solid electrolyte, if the amount is small, the lithium ion conductive crystals High lithium ion conductivity of inorganic substances containing glass or glass ceramics is not observed in solid electrolytes. On the other hand, if the amount is too large, the content of the inorganic substance acting as a binder decreases, the adhesion between the inorganic substance or glass ceramic-inorganic substance including the lithium ion conductive crystal is weak, and the above lithium ion conductive crystal is included. The mobility of lithium ions between inorganic substances or glass ceramic powders is deteriorated, and the strength is also reduced. Therefore, the lower limit of the content of the inorganic substance containing lithium ion conductive crystals or the lithium ion conductive glass ceramic powder in the solid electrolyte of the present invention is preferably 50% by mass, more preferably 60% by mass, and 70% by weight. % Is most preferred. Moreover, as an upper limit, 98 mass% is preferable, 97 mass% is more preferable, and 96 mass% is the most preferable.

The positive electrode of the lithium ion secondary battery of the present invention is configured to include at least a positive electrode active material described later. Moreover, it is preferable that it is the structure containing a positive electrode compound material and a positive electrode electrical power collector. The negative electrode includes at least a negative electrode active material described later. Moreover, it is preferable that it is the structure containing a negative electrode compound material and a negative electrode electrical power collector.
The positive electrode mixture and / or the negative electrode mixture of the lithium ion secondary battery of the present invention may include an active material, an ion conduction aid and / or an electron conduction aid, and a binder for fixing them. preferable.

  Moreover, when producing a positive electrode mixture and / or a negative electrode mixture, it can be produced simply by simply mixing and drying an active material, a conductive additive and a binder using a solvent. (In this specification, this is a simple mixing method.)

From the viewpoint of obtaining a battery with a higher capacity by reducing the addition amount of the ion conduction aid as much as possible, the preparation of the positive electrode mixture and / or the negative electrode mixture is not performed by a simple mixing method, but on the surface of the active material particles. It is more preferable to use a mixing method in which the ion conduction aid and / or the electron conduction aid are fixed by a binder. (In this specification, this is referred to as an immobilization mixing method.)
The positive electrode composite material and the negative electrode composite material undergo a volume change due to desorption and insertion of Li ions from the active material by charge and discharge. Then, due to the expansion and contraction of the active material, the electron conduction aid and the ion conduction aid are gradually peeled off from the active material, and the amount of the active material that cannot be desorbed from Li increases, resulting in cycle deterioration. . If the electron conduction assistant and ion conduction assistant with fine particles are fixed to the active material surface by a binder method, there will be little peeling during expansion and contraction of the active material, and capacity degradation due to charge and discharge will be reduced. It is possible to add an ion conduction auxiliary agent without reducing the battery capacity per unit volume and weight.

As an immobilization mixing method, it is preferable to use the following method. That is, when the active material is flowed or rotated at a high speed, a dispersion obtained by slurrying a conductive additive and a binder using a solvent is charged or sprayed and dried at a temperature equal to or higher than the boiling point of the solvent. When mixing the active material and conduction aid, the larger the difference in particle size, the easier the interactive mixture will occur, and the greater the tendency for finer conduction aids to adhere to the large active material particles. A layer of auxiliaries is formed.
The immobilization mixing method is not limited to this method, and it is also possible to use a method in which an active material and a conduction aid having a sufficiently different particle size are dispersed in a solvent together with a binder, followed by hot air drying and freeze drying. It is also possible to use conventional granulation and surface coating techniques.

  As the active material used for the positive electrode of the lithium ion secondary battery of the present invention, a transition metal compound capable of occluding and releasing lithium can be used. For example, manganese, cobalt, nickel, vanadium, niobium, molybdenum, titanium , Transition metal oxides containing at least one selected from iron and phosphorus can be used. Since most active material materials have poor electron conductivity and ion conductivity, conductive carbon, graphite, carbon fiber, metal powder, metal fiber, electron conductive polymer, etc. should be added as an electron conduction aid. preferable. Moreover, it is preferable to add ion-conductive glass ceramics, ion-conductive polymers, and the like as the ion conduction aid. The addition amount of the electron / ion conduction auxiliary agent is preferably in the range of 3 to 35% by mass, more preferably 2.5 to 30% by mass, and 3 to 25% by mass with respect to the positive electrode active material. Most preferably.

  In this lithium secondary battery, the active material used for the negative electrode includes metal lithium, lithium-aluminum alloy, lithium-indium alloy and other alloys capable of occluding and releasing lithium, and transition metal oxidation such as titanium and vanadium. And carbon materials such as graphite and graphite are preferably used. When the active material has poor electron conductivity, it is preferable to add conductive carbon, graphite, carbon fiber, metal powder, metal fiber, electron conductive polymer or the like as an electron conduction aid. Moreover, it is preferable to add ion-conductive glass ceramics, ion-conductive polymers, and the like as the ion conduction aid. The addition amount of the electron / ion conduction auxiliary agent is preferably in the range of 3 to 35% by mass, more preferably 2.5 to 30% by mass, and 3 to 25% by mass with respect to the negative electrode active material. Most preferably.

  When the positive electrode and / or the negative electrode of the lithium ion secondary battery contains an inorganic substance containing lithium ion conductive crystals or lithium ion conductive glass ceramics as an ion conduction aid, a powder is preferable.

  The average particle size of the inorganic substance containing lithium ion conductive crystals or the lithium ion conductive glass ceramic powder is determined when the positive electrode and / or negative electrode mixture is prepared by a simple mixing method. It is preferably 1/5 or less, more preferably 1/7 or less, and more preferably 1/10 or less of the average particle diameter of the positive electrode and / or negative electrode active material containing an inorganic substance containing crystals or lithium ion conductive glass ceramics. Most preferred. By making the average particle diameter of inorganic materials or glass ceramics containing lithium ion conductive crystals as auxiliary agents sufficiently small compared to the active material, the contact area with the active material is increased and the capacity of the battery is reduced. This is because sufficient ion conductivity is imparted by adding such an amount that does not occur. When the average particle size of the inorganic material or glass ceramic containing lithium ion conductive crystals is the same as or larger than that of the positive electrode and / or negative electrode active material, sufficient ion conductivity is imparted to the positive electrode material and / or the negative electrode material. For this purpose, it is necessary to contain an inorganic substance or glass ceramics containing a large amount of lithium ion conductive crystals. For example, in the case of the same particle size, it is necessary to add an inorganic material or glass ceramic containing a lithium ion conductive crystal in the same amount or more as the active material, and the active material content in the positive electrode material is reduced. A battery with a capacity cannot be obtained.

  In the case of producing a positive electrode mixture and / or a negative electrode mixture by a simple mixing method, an inorganic substance containing lithium ion conductive crystals or lithium ion conductive glass ceramics contained in the positive electrode and / or negative electrode as an ion conduction aid The amount of the inorganic material or lithium ion conductive material containing the lithium ion conductive crystal is necessary to impart sufficient ion conductivity to the positive electrode mixture and / or the negative electrode mixture in order to perform good charge / discharge. It is preferable to set it as 10 mass% or more with respect to the active material of the positive electrode and / or negative electrode containing glass ceramics, it is more preferable to set it as 12 mass% or more, and it is most preferable to set it as 15 mass% or more. On the other hand, when the content of the inorganic material containing lithium ion conductive crystals or the lithium ion conductive glass ceramic is increased, the content of the active material in the positive electrode mixture and / or the negative electrode mixture decreases, and the unit volume or unit Since the battery capacity per weight is reduced, the content is preferably 35% by mass or less, more preferably 30% by mass or less, and most preferably 25% by mass or less.

  When a positive electrode mixture and / or a negative electrode mixture is prepared by an immobilization mixing method, the average particle size of the inorganic substance or lithium ion conductive glass ceramic containing a lithium ion conductive crystal is the lithium ion conductive It is preferably 1/5 or less, more preferably 1/7 or less, of the average particle diameter of the active material of the positive electrode and / or negative electrode containing an inorganic substance containing crystals or lithium ion conductive glass ceramics. Most preferably: The content of the ion conduction auxiliary agent can be obtained in a small amount as compared with the case where the simple mixing method is used. Therefore, in order to obtain a high capacity battery, the content includes the lithium ion conductive crystal. The content is preferably 2% by mass or more, more preferably 2.5% by mass or more, and most preferably 3% by mass or more based on the active material of the positive electrode and / or the negative electrode containing an inorganic substance or lithium ion conductive glass ceramics. In order to contain a large amount of the active material, the upper limit of the inorganic substance containing lithium ion conductive crystals or the lithium ion conductive glass ceramic is preferably 15% by mass or less, more preferably 12% by mass or less, and most preferably 10% by mass or less. . The same applies to the electron conduction assistant, and by making the particle diameter of the conduction assistant smaller, the effect of imparting conductivity equal to or higher than that of the conventional one can be obtained with a smaller amount.

  The inorganic substance or ion conductive glass ceramic containing lithium ion conductive crystals contained in the positive electrode and the negative electrode may be the same as the inorganic substance or glass ceramic containing lithium ion conductive crystals contained in the solid electrolyte. More preferred. If they are the same, the ion transfer mechanism contained in the electrolyte and the electrode material is unified, so that ion transfer between the electrolyte and the electrode can be performed smoothly, and a battery with higher output and higher capacity can be provided. Here, an inorganic substance or glass ceramic containing the same lithium ion conductive crystal means an inorganic substance or glass ceramic containing a lithium ion conductive crystal having the same crystal system. An inorganic substance or glass ceramic containing a lithium ion conductive crystal mainly responsible for ion migration in an electrode has the same movement mechanism as an inorganic substance or glass ceramic containing a lithium ion conductive crystal contained in an electrolyte. , All the ion migration paths in the battery become equal, and the ion migration barrier becomes smaller.

PVdF, PTFE, SBR rubber, etc. can be used as the binder used when preparing and preparing a positive electrode mixture and / or negative electrode mixture by mixing and binding an active material and a conduction aid. It is more preferable to use an ion conductive binder.
Here, a polymer material can be used as the ion conductive binder. For example, polyethylene oxide, polypropylene oxide, fluorine resin (polyolefin, polytetrafluoroethylene, polychlorotrifluoroethylene, polyvinylidene fluoride, etc.), polyamides, polyester polyacrylates and copolymers thereof, and cross-linked structures thereof , Or mixtures thereof, and any Li salt for these polymers, for example, LiBF ₄ , LiSO ₃ CF ₃ , LiSO ₃ CH ₃ , LiN (SO ₂ CF ₃ ) ₂ , LiN (SO ₂ A binder imparted with ionic conductivity by adding C ₂ F ₅ ) ₂ , LiC (SO ₂ CF ₃ ) ₃ , organic ionic polysulfide, or the like can be used.

  According to the present invention, in an all-solid-state lithium ion secondary battery having no leakage problem, the heat resistant temperature is high, it can be used in a wide temperature range, the battery capacity is high, and the charge / discharge cycle characteristics are also high. It is possible to provide a solid electrolyte or an all solid-state lithium secondary battery that is good and can be used stably over a long period of time.

  Hereinafter, a solid electrolyte containing an inorganic substance containing lithium ion conductive crystals or a lithium ion conductive glass ceramic according to the present invention and a lithium ion secondary battery using the same will be described with specific examples. In addition, a comparative example is given and it is clear that a solid electrolyte containing a lithium ion conductive glass ceramic and an inorganic substance containing lithium ion conductive crystals according to this example and a lithium ion secondary battery including the same are excellent. To. In addition, this invention is not limited to what was shown to the following Example, In the range which does not change the summary, it can change suitably and can implement.

[Example 1]
(Production of lithium ion conductive glass ceramics)
H ₃ PO ₄ , Al (PO ₃ ) ₃ , Li ₂ CO ₃ , SiO ₂ , and TiO ₂ are used as raw materials, and these are mol% in terms of oxide, P ₂ O ₅ is 35.0%, Al ₂ O ₃ is 7.5%, Li ₂ O is 15.0%, TiO ₂ is 38.0% and SiO ₂ is 4.5%. Then, the glass melt was heated and melted at 1500 ° C. in an electric furnace for 3 hours while stirring. Thereafter, the glass melt was formed into a thin plate having a thickness of 0.3 mm with a stainless steel molding machine, and crystallized by heat treatment at 950 ° C. for 12 hours to produce a thin plate of glass ceramics.
Further, a glass melt having the same composition was dropped into running water to obtain flaky glass, which was crystallized by heat treatment at 950 ° C. for 12 hours to obtain glass ceramics. The obtained glass ceramic flakes were pulverized by a ball mill to obtain a glass ceramic fine powder A having an average particle diameter of 1.5 μm and a maximum particle diameter of 7 μm. The fine powder A was further finely pulverized by a wet ball mill to obtain a slurry B containing glass ceramic fine powder having an average particle size of 0.2 μm and a maximum particle size of 0.3 μm.
These glass ceramics have Li _{1 + x + y} Al _x Ti _{2 -x} Si _y P ₃ -yO ₁₂ (0 ≦ x ≦ 0.4, 0 <y ≦ 0.6) as the main crystal phase by powder X-ray diffraction method. It was confirmed that there was.
(Production of solid electrolyte)
The glass ceramic thin plate obtained above was polished to a thickness of 40 μm and punched to a diameter of 16 mm to produce a solid electrolyte.
(Preparation of positive electrode)
Commercially available lithium cobalt oxide LiCoO2 (average particle size 6 μm) as the positive electrode active material, acetylene black (average particle size 50 nm) as the electron conduction auxiliary agent 5 mass% with respect to the positive electrode active material, and LiBF as the binder Polyethylene oxide added with ₄ and a polymer of polypropylene oxide were mixed using an ethanol solvent using a vacuum stirring deaerator. This mixture was uniformly applied on an aluminum sheet as a positive electrode current collector having a thickness of 16 μm, and then dried at a temperature of 120 ° C. to produce a positive electrode. The thickness of the positive electrode mixture was 30 μm, and this was punched into a diameter of 15 mm to produce a positive electrode.
(Preparation of negative electrode)
For the production of the negative electrode, a commercially available graphite powder (average particle size 10 μm) as a negative electrode active material and a polymer of polyethylene oxide and polypropylene oxide added with LiBF ₄ as a binder were removed by stirring under vacuum. Mix using a foam apparatus. This mixture was applied to a 12 μm-thick copper sheet as a negative electrode current collector, and then dried at a temperature of 120 ° C. to produce a sheet-like negative electrode. The thickness of the negative electrode material was 20 μm, and this was punched out to a diameter of 15 mm to produce a negative electrode.
(Battery assembly)
The above positive electrode, electrolyte, and negative electrode were sequentially stacked, uniaxially pressed in a dry atmosphere at 150 ° C., and then sealed in a coin cell. A cross-sectional view of the internal structure of this battery is shown in FIG.
The assembled battery was subjected to charge / discharge measurement at a room temperature of 25 ° C. with a constant current of 100 μA / cm ² , a charge of 4.2 V, and a discharge of 3.0 V. The initial discharge capacity was 0.80 mAh, and the discharge capacity after repeating 20 cycles was 0.56 mAh, which was 70% of the initial capacity.

[Example 2]
A positive electrode and a negative electrode were mixed with a glass ceramic fine powder slurry B in a solid content of 20% by mass with respect to the positive electrode active material and the negative electrode active material, respectively. The charge / discharge measurement was performed under the same conditions. The initial discharge capacity was 1.20 mAh, and the discharge capacity after repeating 20 cycles was 1.15 mAh, which was 96% of the initial capacity.

  In Examples 1 and 2, the initial discharge capacity is large, and the capacity deterioration associated with the charge / discharge cycle is small. Example 2 in which lithium ion conductive glass ceramics were contained in the positive electrode and the negative electrode showed particularly good values.

[Example 3]
(Production of solid electrolyte)
The glass ceramic powder A obtained in Example 1 and 5% by mass of Li ₃ PO ₄ were mixed and formed into a pellet shape of φ20 mm using CIP (Cold Isostatic Press). The molded pellets were sintered at 1000 ° C. using HIP (Hot Isostatic Press), then ground and polished to produce a solid electrolyte having a diameter of 16 mm and a thickness of 0.08 mm. Here, a liquid phase sintering method is used in which Li ₃ PO ₄ melts and binds glass ceramics that is powder.
(Preparation of positive electrode)
A commercially available fluidized granulator was used for producing the positive electrode mixture. 5% by mass of ketjen black (average particle size of 40 nm) as an electron conduction aid with respect to the positive electrode active material, and glass ceramic fine powder A having an average particle size of 1.5 μm as an ion conduction aid (in Example 1) Preparation) was mixed with 10 mass% of the positive electrode active material, and a polymer of polyethylene oxide and polypropylene oxide added with LiTFSI as a binder using an ethanol solvent to prepare a spray suspension.
As the positive electrode active material, commercially available lithium manganate LiMn ₂ O ₄ (average particle size 10 μm) is used, and this positive electrode active material is placed in a fluid granulator and fluidized at a temperature of 90 ° C. On the other hand, the prepared spray suspension was sprayed, and ethanol as a solvent was volatilized to fix the electron conduction assistant and the ion conduction assistant on the particle surface of the active material. This surface-covered positive electrode mixture was lightly dispersed again using ethanol and uniformly applied onto an aluminum sheet as a positive electrode current collector having a thickness of 20 μm, and then dried again at a temperature of 120 ° C. A positive electrode was produced. The thickness of the positive electrode mixture was 35 μm, and this was punched into a diameter of 15 mm to produce a positive electrode.
(Preparation of negative electrode)
For the production of the negative electrode mixture, the same commercially available fluidized granulator as the positive electrode material was used. 5% by mass of ketjen black (average particle size of 40 nm) as an electron conduction aid with respect to the negative electrode active material, and glass ceramic fine powder A having an average particle size of 1.5 μm as an ion conduction aid (in Example 1) Preparation) was mixed with 10 mass% of the negative electrode active material, and a polymer of polyethylene oxide and polypropylene oxide added with LiTFSI as a binder using an ethanol solvent to prepare a spray suspension.
As the negative electrode active material, a commercially available lithium titanate Li ₄ Ti ₅ O ₁₂ was granulated to have an average particle size of 3 μm. This negative electrode active material is put into a fluidized granulator, the prepared spray suspension is sprayed on the negative electrode active material flowing at a temperature of 90 ° C., and ethanol as a solvent is volatilized. An electron conduction aid and an ion conduction aid were fixed on the particle surface. After the surface-coated negative electrode mixture was lightly dispersed again using ethanol and uniformly applied onto a copper sheet as a negative electrode current collector having a thickness of 18 μm, this was again dried at a temperature of 120 ° C. A negative electrode was produced. The thickness of the negative electrode mixture was 25 μm, and this was punched into a diameter of 15 mm to produce a positive electrode.
(Battery assembly)
The above positive electrode, electrolyte, and negative electrode were sequentially stacked, uniaxially pressed in a dry atmosphere at 150 ° C., and then sealed in a coin cell. The assembled battery was subjected to charge / discharge measurement at a room temperature of 25 ° C. with a constant current of 60 μA / cm ² , a charge of 4.0 V, and a discharge voltage of 3.0 V. The initial discharge capacity was 0.95 mAh, and the discharge capacity after repeating 20 cycles was 0.76 mAh, which was 70% of the initial capacity.

[Example 4]
Instead of the glass ceramic fine powder A used for each of the positive electrode and the negative electrode of Example 3, the slurry B prepared in Example 1 was used as an ion conduction aid for the positive electrode and the negative electrode with respect to the positive electrode active material and the negative electrode active material, respectively. The battery was assembled with the same manufacturing method and configuration as the battery of Example 3 except that 5% by mass was used as the solid content, and charge / discharge measurement was performed under the same conditions as in Example 3. The initial discharge capacity was 1.43 mAh, and the discharge capacity after repeating 20 cycles maintained 1.31 mAh, which was 92% of the initial capacity.

The change of the discharge capacity accompanying the charging / discharging cycle of Example 3 and Example 4 was shown in FIG.
In Examples 3 and 4, the initial discharge capacity is large, and the capacity deterioration associated with the charge / discharge cycle is small. Example 4 in which the particle size of the lithium ion conductive glass ceramic contained in the positive electrode and the negative electrode was smaller showed a particularly good value.

[Example 5]
(Preparation of positive electrode)
A commercially available spray drying apparatus was used for producing the positive electrode mixture. Cobalt-substituted lithium cobaltate LiNi _0.8 Co _0.2 O ₂ (average particle size 3 μm) as an active material for the positive electrode and carbon nanofibers (average diameter 80 nm) as an electron conduction aid for the positive electrode active material 2% by mass, 4% by mass of SiO ₂ fine powder having an average particle diameter of 50 nm with respect to the positive electrode active material, and a polymer of polyethylene oxide and polypropylene oxide to which LiTFSI is added as a binder are mixed with methanol and ethanol. The suspension was prepared by mixing with a solvent. The suspension was spray-dried with a spray-drying apparatus while stirring, and the solvent was volatilized to fix the electron conduction aid and the ion conduction aid on the surface of the active material particles. The surface-covered positive electrode mixture was lightly dispersed using an ethanol solvent, and uniformly applied onto an aluminum sheet as a positive electrode current collector having a thickness of 20 μm, and then dried again at a temperature of 120 ° C. A positive electrode was produced. The thickness of the positive electrode mixture was 40 μm, and this was punched into a diameter of 15 mm to produce a positive electrode.
(Preparation of negative electrode)
For the production of the negative electrode mixture, the same commercially available spray drying apparatus as that for the positive electrode material was used. As a negative electrode active material, commercially available lithium titanate Li ₄ Ti ₅ O ₁₂ was granulated to have an average particle size of 3 μm, and carbon nanofibers (average diameter of 80 nm) as an electron conduction aid were used as the negative electrode active material. On the other hand, 2% by mass, 3% by mass of SiO ₂ fine powder having an average particle diameter of 50 nm with respect to the negative electrode active material, and a polymer of polyethylene oxide and polypropylene oxide to which LiTFSI was added as a binder were combined with methanol and ethanol. The mixed solvent was used to prepare a suspension. The suspension was spray-dried with a spray-drying apparatus while stirring, and the solvent was volatilized to fix the electron conduction aid and the ion conduction aid on the surface of the active material particles. The surface-covered negative electrode mixture was lightly dispersed using an ethanol solvent, and uniformly coated on a copper sheet as a negative electrode current collector having a thickness of 18 μm, and then dried again at a temperature of 120 ° C. A negative electrode was produced. The thickness of the negative electrode mixture was 40 μm, and this was punched into a diameter of 15 mm to produce a positive electrode.
(Battery assembly)
The above positive electrode, the electrolyte prepared in Example 4 and the negative electrode were sequentially superposed, uniaxially pressed in a dry atmosphere at 150 ° C., and sealed in a coin cell. The assembled battery was subjected to charge / discharge measurement at a room temperature of 25 ° C. with a constant current of 60 μA / cm ² , a charge of 4.0 V, and a discharge voltage of 3.0 V. The initial discharge capacity was 0.58 mAh, and the discharge capacity after repeating 20 cycles was 0.46 mAh, which was about 80% of the initial capacity.

[Example 6]
In the battery of Example 5, instead of the SiO ₂ fine powder having an average particle diameter of 50 nm contained in each of the positive electrode and the negative electrode, a glass ceramic fine powder slurry B (prepared in Example 1) as an ion conduction aid was used for the positive electrode. The battery was assembled with the same production method and configuration as the battery of Example 5 except that 4% by mass in solid content with respect to the positive electrode active material and 3% by mass with respect to the negative electrode active material were used for the negative electrode. The charge / discharge measurement was performed under the conditions. The initial discharge capacity was 2.18 mAh, and the discharge capacity after 20 cycles was maintained at 2.07 mAh, which was 95% of the initial capacity.

The change of the discharge capacity accompanying the charging / discharging cycle of Example 5 and Example 6 was shown in FIG.
In Examples 5 and 6, the initial discharge capacity is large, and the capacity deterioration associated with the charge / discharge cycle is also small. Example 6 in which lithium ion conductive glass ceramics were contained in the positive electrode and the negative electrode showed particularly good values.

[Example 7]
(Preparation of positive electrode)
Commercially available lithium cobaltate LiCoO ₂ (average particle size 6 μm) was used as the positive electrode active material, and a high-speed processing apparatus was used for the production of the positive electrode mixture. Polyethylene in which lithium cobaltate was mixed at a high speed of 5000 rpm, and ketjen black (average particle size 40 nm) as an electron conduction aid was added to 5% by mass with respect to the positive electrode active material, and LiBF ₄ was added as a binder. An ethanol solvent in which a polymer of oxide and polypropylene oxide is dispersed in an amount of 9% by mass with respect to the positive electrode active material is sprayed little by little, a conductive agent is embedded in the positive electrode active material, and vacuum dried at 120 ° C. A positive electrode mixture was produced.
(Preparation of negative electrode)
A metal Li foil having a thickness of 0.2 mm with a Cu film formed on the surface by sputtering was punched into a size of φ15 mm to obtain a negative electrode material.
(Battery assembly)
The positive electrode prepared above, the solid electrolyte prepared in Example 4, and the negative electrode were stacked, uniaxially pressed in a dry atmosphere at 150 ° C., and sealed in a coin-type cell to assemble a coin battery.
The assembled battery was subjected to charge / discharge measurement at a room temperature of 25 ° C. and 80 ° C. with a constant current of 0.1 mA / cm ² , a charge of 4.2 V, and a discharge of 3.0 V. The initial discharge capacity at 25 ° C. was 2.9 mAh, and the discharge capacity after repeating 20 cycles was 2.5 mAh, maintaining the initial capacity of 85%. The initial discharge capacity at 80 ° C. was 4.2 mAh, and the discharge capacity after 20 cycles was maintained at 3.9 mAh, which was 90% of the initial capacity.

[Example 8]
In the battery of Example 7, polyethylene oxide and polypropylene containing LiBF ₄ added to the positive electrode containing further 7% by mass of a solid powder slurry B of glass ceramic (produced in Example 1) in solid content with respect to the positive electrode active material. A battery having the same manufacturing method and configuration as in Example 7 was assembled except that the content of the oxide polymer was 2% by mass with respect to the positive electrode active material. As a result of charge / discharge measurement under the same conditions as in Example 7, the initial discharge capacity at 25 ° C. was 4.1 mAh, and the discharge capacity after 20 cycles was 3.9 mAh, which is 95% of the initial value. The capacity of was maintained. The initial discharge capacity at 80 ° C. was 4.5 mAh, and the discharge capacity after repeating 20 cycles was 4.1 mAh, maintaining the initial 90% capacity.
A comparison of the discharge capacities of Example 7 and Example 8 is shown in Table 1. In Examples 7 and 8, the initial discharge capacity is large, and the capacity deterioration associated with the charge / discharge cycle is small. Example 8 in which lithium ion conductive glass ceramic was contained in the positive electrode showed a particularly good value at room temperature of 25 ° C.

[Comparative example]
(Production of solid electrolyte)
A material obtained by grinding LiI, which is an ion conductive ceramic, to an average particle size of 2 μm was formed into a pellet shape of φ20 mm using CIP. The molded pellets were sintered at 350 ° C., and then ground and polished to produce a solid electrolyte having a diameter of 16 mm and a thickness of 0.08 mm.
(Battery assembly)
The same positive electrode as in Example 7, the solid electrolyte prepared above, and the same negative electrode as in Example 7 were stacked and uniaxially pressed, and sealed in a coin-type cell to assemble a coin battery. Charge and discharge measurements were performed at a room temperature of 25 ° C. with a constant current of 0.1 mA / cm 2, a charge of 4.2 V, and a cut-off voltage of 3.0 V. The initial discharge capacity was 1.1 mAh, and the discharge capacity after repeating 20 cycles was as large as 0.3 mAh.

  As described above, the lithium ion secondary battery containing the lithium ion conductive glass ceramic of the present invention is a battery having high output and good charge / discharge cycle characteristics even if it is an all solid battery not containing an organic electrolyte. It can be seen that it is.

  Since the electrolyte of the present invention containing an inorganic compound and lithium ion conductive glass ceramics has high lithium ion conductivity and is electrochemically stable, not only an electrolyte for a lithium ion secondary battery but also a lithium primary battery or Applications to electrochemical capacitors called hybrid capacitors, dye-sensitized solar cells, and other electrochemical devices using lithium ions as charge transfer carriers are also possible.

Some examples of other electrochemical elements are given below.
By attaching an arbitrary sensitive electrode on the electrolyte, it can be applied to various gas sensors and detectors. For example, a carbonate gas sensor can be applied to a carbon dioxide gas sensor, a nitrate-containing electrode can be applied to a NOx sensor, and a sulfate-containing electrode can be applied to a SOx sensor. Further, by incorporating an electrolytic cell, it can be applied to an electrolyte for a decomposition / collection device such as NOx and SOx contained in exhaust gas.

  An electrochromic device can be configured by attaching an inorganic compound or organic compound that is colored or discolored by insertion and removal of Li ions on the electrolyte, and by attaching a transparent electrode such as ITO thereon. An electrochromic display having a memory property can be provided.

  Since the ion conduction path of the electrolyte of the present invention has an optimum size for lithium ions, lithium ions can be selectively passed even when other alkali ions are present. Therefore, it can be used as a diaphragm for a lithium ion selective collection device or a diaphragm for a Li ion selective electrode. Moreover, since the speed of the lithium ion which permeate | transmits is so high that the mass of ion is small, it can apply to the isotope separation of lithium ion. This makes it possible to concentrate and separate the concentrated 6Li (7.42% in natural abundance) necessary for the tritium production blanket material for fusion reactor fuel.

  The lithium ion conductive glass ceramic powder contained in the electrolyte and the electrode material has high lithium ion conductivity and is electrochemically stable. Therefore, by kneading into other resins and paints, imparting ion conductivity, It can be used as an additive for antistatic and surface potential control.

It is sectional explanatory drawing which showed the internal structure of an example of the lithium ion secondary battery of this invention. It is a change of the discharge capacity accompanying the charging / discharging cycle of the lithium ion secondary battery obtained in Example 1 and Example 2. FIG. It is a change of the discharge capacity accompanying the charging / discharging cycle of the lithium ion secondary battery obtained in Example 3 and Example 4. FIG. It is a change of the discharge capacity accompanying the charging / discharging cycle of the lithium ion secondary battery obtained in Example 5 and Example 6. FIG.

Explanation of symbols

1: Positive current collector 2: Positive electrode mixture 3: Solid electrolyte 4: Negative electrode mixture 5: Negative electrode current collector

Claims (7)

A powder of lithium ion conductive glass ceramics containing a lithium ion conductive crystal, and an inorganic compound selected from Li ₃ PO ₄ , LiPO ₃ , LiI, LiN, Li ₂ O, Li ₂ O ₂ and LiF. A solid electrolyte characterized in that it contains no organic matter and no electrolyte solution and is sintered, and the content of the powder is 50 wt% to 98 wt%.   2. The solid electrolyte according to claim 1, wherein the powder does not contain vacancies or grain boundaries that inhibit ion conduction. 2. The solid electrolyte according to claim 1, wherein the powder has an ionic conductivity of 10 ⁻⁴ Scm ⁻¹ or more and an average particle size of 9 μm or less. Solid electrolyte according to any one of claims 1 to 3, characterized in that the ionic conductivity is ¹⁰ -5 ^{Scm -1} or higher. The powder is the main crystalline phase is _{Li 1 + x + y Al x} Ti 2-x Si y P 3-y O 12 where the claim 1, characterized in that the 0 ≦ x ≦ 1,0 ≦ y ≦ 1 4 The solid electrolyte according to any one of the above. The powder is expressed in mol%,
Li ₂ O: 12~18%, and _{Al 2 O 3 + Ga 2 O} 3: 5~10%, and _{TiO 2 + GeO 2: 35~45%} , and SiO _2: 1~10%, and P ₂ O _5: 30-40%
Each of these components is contained, The solid electrolyte in any one of Claim 1 to 5 characterized by the above-mentioned. Lithium-ion secondary battery characterized by comprising a solid electrolyte according to any one of claims 1 to 6.

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