WO2009139382A1 - 固体電解質、その製造方法、および固体電解質を備える二次電池 - Google Patents
固体電解質、その製造方法、および固体電解質を備える二次電池 Download PDFInfo
- Publication number
- WO2009139382A1 WO2009139382A1 PCT/JP2009/058835 JP2009058835W WO2009139382A1 WO 2009139382 A1 WO2009139382 A1 WO 2009139382A1 JP 2009058835 W JP2009058835 W JP 2009058835W WO 2009139382 A1 WO2009139382 A1 WO 2009139382A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- solid electrolyte
- libh
- alkali metal
- lii
- temperature
- Prior art date
Links
Images
Classifications
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M10/00—Secondary cells; Manufacture thereof
- H01M10/05—Accumulators with non-aqueous electrolyte
- H01M10/056—Accumulators with non-aqueous electrolyte characterised by the materials used as electrolytes, e.g. mixed inorganic/organic electrolytes
- H01M10/0561—Accumulators with non-aqueous electrolyte characterised by the materials used as electrolytes, e.g. mixed inorganic/organic electrolytes the electrolyte being constituted of inorganic materials only
- H01M10/0562—Solid materials
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01B—CABLES; CONDUCTORS; INSULATORS; SELECTION OF MATERIALS FOR THEIR CONDUCTIVE, INSULATING OR DIELECTRIC PROPERTIES
- H01B1/00—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors
- H01B1/06—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors mainly consisting of other non-metallic substances
- H01B1/12—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors mainly consisting of other non-metallic substances organic substances
- H01B1/122—Ionic conductors
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M10/00—Secondary cells; Manufacture thereof
- H01M10/05—Accumulators with non-aqueous electrolyte
- H01M10/052—Li-accumulators
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M2300/00—Electrolytes
- H01M2300/0017—Non-aqueous electrolytes
- H01M2300/0065—Solid electrolytes
- H01M2300/0068—Solid electrolytes inorganic
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M2300/00—Electrolytes
- H01M2300/0088—Composites
- H01M2300/0091—Composites in the form of mixtures
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
- Y02E60/10—Energy storage using batteries
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P70/00—Climate change mitigation technologies in the production process for final industrial or consumer products
- Y02P70/50—Manufacturing or production processes characterised by the final manufactured product
Definitions
- the present invention relates to a solid electrolyte and a method for producing the same, and more particularly to a lithium ion conductive solid electrolyte and a method for producing the same. Moreover, this invention relates to a secondary battery provided with such a solid electrolyte.
- lithium ion secondary batteries are known as the batteries with the highest energy density.
- an organic solvent electrolytic solution exhibiting high ion conductivity is used as an electrolyte.
- the organic solvent electrolyte is liquid and flammable, there is a risk of liquid leakage or ignition when used as an electrolyte of a lithium ion secondary battery, and there is concern about its safety. For this reason, a safer solid electrolyte has been demanded as an electrolyte of a lithium ion secondary battery.
- Patent Document 1 discloses a solid electrolyte using lithium ion conductive sulfide-based crystallized glass containing lithium, phosphorus, and sulfur elements as raw materials.
- Patent Document 2 discloses each element of lithium, phosphorus, sulfur and oxygen, and an element belonging to any one of Groups 13 to 16 in the periodic table (however, phosphorus, sulfur And a solid electrolyte containing oxygen) is disclosed.
- LiBH 4 exhibits high ionic conductivity at a high temperature of about 117 ° C. (about 390 K) or higher [M. Matsuo, Y. et al. Nakamori, S .; Orimo, H .; Maekawa, and H.M. Takamura, Appl. Phys. Lett. 2007, Vol. 91, 224103 (Non-patent Document 1)].
- LiBH 4 has a high resistance at a temperature lower than 115 ° C. (388 K), which is the transition temperature of its high ion conduction phase (high temperature phase), and is low in temperature, particularly near room temperature, for use as an electrolyte of a lithium ion secondary battery. There was a problem of low ionic conductivity.
- the present invention has been made in view of the aforesaid problems, to provide a LiBH 4 based solid electrolytes having a high ion conductivity even at below the transition temperature of the high-temperature phase of LiBH 4 (115 °C) Objective.
- the present inventors have mixed LiBH 4 and a specific alkali metal compound, and heated the mixture to melt or sinter it, thereby melting or sintering the mixture.
- the transition temperature of the high-temperature phase of the precipitate decreased, and it was found that high ionic conductivity was exhibited even below the transition temperature of LiBH 4 , and the present invention was completed.
- the solid electrolyte of the present invention includes LiBH 4 and the following formula (1): MX (1)
- M represents an alkali metal atom
- X represents a halogen atom
- an NR 2 group R represents a hydrogen atom or an alkyl group
- an N 2 R group R represents a hydrogen atom or an alkyl group
- Such a solid electrolyte is useful as a solid electrolyte for a lithium ion secondary battery.
- the solid electrolyte of the present invention includes LiBH 4 and the following formula (1): MX (1)
- M represents an alkali metal atom
- X represents a halogen atom
- an NR 2 group represents a hydrogen atom or an alkyl group
- an N 2 R group represents a hydrogen atom or an alkyl group
- the heating temperature of the said mixture is 50 degreeC or more normally.
- the solid electrolyte thus obtained is preferably heated at 115 ° C. or higher and then cooled. This tends to increase the ionic conductivity of the solid electrolyte below the transition temperature of the high temperature phase of LiBH 4 .
- X in the formula (1) is preferably any one of an iodine atom and an amino group, and the alkali metal compound is at least one selected from the group consisting of LiI, RbI and CsI. Is more preferable.
- the transition temperature of the high-temperature phase is low, it is possible to provide a LiBH 4 based solid electrolytes having a high ion conductivity even at below the transition temperature of the high-temperature phase of LiBH 4 (115 °C).
- FIG. 3 is a graph showing X-ray diffraction patterns of solid electrolytes comprising LiBH 4 and LiI obtained in Examples 1 to 3. It is a graph which shows the relationship between the ionic conductivity of the solid electrolyte obtained in Example 4 and Comparative Example 1, and measurement temperature.
- 6 is a graph showing the relationship between the ionic conductivity of the solid electrolytes obtained in Examples 4 to 5 and Comparative Example 1 and the measurement temperature. 6 is a graph showing a 7 Li-NMR spectrum of the solid electrolyte obtained in Example 4.
- FIG. 2 is a graph showing a 7 Li-NMR spectrum of a solid electrolyte obtained in Comparative Example 1.
- FIG. 6 is a graph showing the relationship between 7 Li-NMR longitudinal relaxation time and measurement temperature of the solid electrolytes obtained in Example 4 and Comparative Example 1.
- FIG. 6 is a graph showing X-ray diffraction patterns of solid electrolytes comprising LiBH 4 , LiI, and RbI obtained in Examples 6 to 8.
- 10 is a graph showing the relationship between the ionic conductivity of the solid electrolyte obtained in Example 9 and the measurement temperature.
- 6 is a graph showing a 7 Li-NMR spectrum of the solid electrolyte obtained in Example 9.
- FIG. 6 is a graph showing the relationship between 7 Li-NMR longitudinal relaxation time and measurement temperature of the solid electrolyte obtained in Example 9.
- FIG. It is a graph which shows the relationship between the ionic conductivity of the solid electrolyte obtained in Example 10, and measurement temperature.
- 6 is a graph showing the relationship between the ionic conductivity of the solid electrolytes obtained in Examples 11 to 12 and the measurement temperature.
- the solid electrolyte of the present invention includes LiBH 4 and the following formula (1): MX (1)
- M represents an alkali metal atom
- X represents a halogen atom
- an NR 2 group represents a hydrogen atom or an alkyl group
- an N 2 R group represents a hydrogen atom or an alkyl group
- LiBH 4 is not particularly limited, and a conventionally known one used as a reducing agent or a hydrogen storage medium can be used.
- the purity of LiBH 4 is preferably 80% or more, and more preferably 90% or more. When the purity of LiBH 4 is less than the lower limit, the performance of the solid electrolyte tends to decrease.
- the alkali metal compound used in the present invention is represented by the formula (1), and M in the formula (1) is a lithium atom (Li), a sodium atom (Na), or a potassium atom (K).
- M in the formula (1) is a lithium atom (Li), a sodium atom (Na), or a potassium atom (K).
- the halogen atom as X in the formula (1) include an iodine atom (I), a bromine atom (Br), a fluorine atom (F), and a chlorine atom (Cl).
- R in the NR 2 group or N 2 R group include a hydrogen atom and an alkyl group, and the alkyl group preferably has 1 to 5 carbon atoms.
- the two Rs in the NR 2 group may be the same or different.
- the alkali metal atom is preferably a lithium atom, a rubidium atom, or a cesium atom.
- X in the formula (1) is preferably an iodine atom, bromine atom or NR 2 group, more preferably an iodine atom or NH 2 group.
- alkali metal compounds may be used alone or in combination of two or more.
- alkali metal halides and amine salts are preferable in that the performance of the solid electrolyte is further improved.
- Lithium halides such as LiI, LiBr, LiF and LiCl; halogens such as RbI, RbBr, RbF and RbCl Rubidium chloride; cesium halides such as CsI, CsBr, CsF, and CsCl; aminolithium such as LiNH 2 , LiNHR, and LiNR 2 is more preferable, LiI, RbI, CsI, and LiNH 2 are particularly preferable, and LiI and RbI may be used in combination. Most preferred.
- the purity of the alkali metal compound is preferably 80% or more, more preferably 90% or more. When the purity of the alkali metal compound is less than the lower limit, the performance of the solid electrolyte tends to deteriorate.
- the molar ratio is less than the lower limit, the proportion of LiBH 4 in the solid electrolyte is small, and high ionic conductivity tends to be difficult to obtain.
- the upper limit is exceeded, the addition effect of the alkali metal compound, that is, high temperature The transition temperature of the phase (high ionic conduction phase) is unlikely to decrease, and the ionic conductivity tends to not increase sufficiently below the transition temperature (115 ° C.) of the high temperature phase of LiBH 4 .
- the content ratio is not particularly limited.
- LiI and another alkali metal compound preferably RbI or CsI
- LiI: other Of the alkali metal compound is preferably 1: 1 to 20: 1, more preferably 5: 1 to 20: 1.
- the molar ratio is less than the lower limit, the proportion of LiI in the solid electrolyte is small, and the thermal stability of the solid electrolyte tends to decrease.
- the upper limit is exceeded, the effect of adding other alkali metal compounds is increased. It cannot be obtained sufficiently, and the ionic conductivity tends not to increase sufficiently.
- At least 2 ⁇ 23.6 ⁇ 0.5 deg, 24.9 ⁇ 0.5 deg, 26.7 ⁇ 0.5 deg, 34.6 ⁇ 0.5 deg, 40.9 ⁇ 0.5 deg. Diffraction in 5 places
- at least 2 ⁇ 23.6 ⁇ 0.3 deg, 24.9 ⁇ 0.3 deg, 26.7 ⁇ 0.3 deg, 34.6 ⁇ 0.3 deg, 40. It is particularly preferable to have a diffraction peak at 5 locations of 9 ⁇ 0.3 deg.
- Diffraction peaks of these five areas which corresponds to the diffraction peak of the high-temperature phase of LiBH 4, a solid electrolyte having a diffraction peak in this 5 region at below the transition temperature of the high-temperature phase of LiBH 4, the It tends to exhibit high ionic conductivity even below the transition temperature.
- the solid electrolyte of the present invention is produced by mixing the LiBH 4 and the alkali metal compound represented by the formula (1), heating and melting or sintering the obtained mixture, and then cooling.
- a method of performing melt mixing is preferable in that a solid electrolyte uniformly including LiBH 4 and the alkali metal compound can be obtained.
- the mixing molar ratio of LiBH 4 and the alkali metal compound is preferably 1: 1 to 20: 1, and more preferably 1: 1 to 10: 1.
- the molar ratio is less than the lower limit, the proportion of LiBH 4 in the obtained solid electrolyte decreases, and it tends to be difficult to obtain a solid electrolyte exhibiting high ionic conductivity.
- the upper limit is exceeded, it is obtained.
- the transition temperature of the high-temperature phase (high ionic conduction phase) of the solid electrolyte is unlikely to decrease, and it tends to be difficult to obtain a solid electrolyte exhibiting high ionic conductivity even below the transition temperature (115 ° C.) of the high-temperature phase of LiBH 4 .
- the heating temperature of the mixture is usually 50 ° C. or higher, preferably 150 ° C. or higher, more preferably 200 ° C. or higher, particularly preferably 250 ° C. or higher, and most preferably 300 ° C. or higher. If the heating temperature is less than the lower limit, the mixture tends to be insufficiently melted or sintered. In particular, the heating temperature when sintering the mixture is usually 50 to 240 ° C., preferably 150 to 240 ° C., more preferably 200 to 240 ° C.
- the mixture of LiBH 4 and the alkali metal compound when the solid electrolyte is molded into a predetermined shape, the mixture of LiBH 4 and the alkali metal compound may be molded in advance and then heated, or may be molded after heating.
- a mixture of LiBH 4 and the alkali metal compound may be formed into a predetermined shape by press molding or the like, then heated and melted or sintered while maintaining this shape, and then cooled.
- a mixture of LiBH 4 and the alkali metal compound is heated and melted, the molten mixture is molded into a predetermined shape and cooled, or the mixture of LiBH 4 and the alkali metal compound is heated and sintered.
- the sintered product may be cooled and then formed into a predetermined shape.
- the manufacturing method of the solid electrolyte of this invention it is preferable to heat the solid electrolyte obtained in this way to 115 degreeC or more, and to cool after that. This tends to increase the ionic conductivity of the solid electrolyte below the transition temperature of the high temperature phase of LiBH 4 .
- the secondary battery of the present invention comprises the solid electrolyte of the present invention, a positive electrode, and a negative electrode.
- the positive electrode material include conventionally known positive electrode materials for lithium ion secondary batteries such as lithium cobaltate, lithium nickelate, and lithium manganate.
- the negative electrode material include conventionally known lithium ion secondary materials such as carbon materials.
- the negative electrode material for secondary batteries include.
- the positive electrode material is applied to one surface of a solid electrolyte formed into a film to form a positive electrode
- the negative electrode material is applied to the other surface to form a negative electrode
- the film-like positive electrode material can be attached to one surface of a solid electrolyte formed into a film shape
- the film-like negative electrode material can be attached to the other surface.
- the result is shown in FIG. FIG. 1 also shows the X-ray diffraction spectrum of LiBH 4 in the high-temperature phase (high ion conduction phase) and the low-temperature phase, and the X-ray diffraction spectrum of LiI.
- An ion conductivity measurement cell was prepared by attaching lithium foil as an electrode on both sides of the solid electrolyte membrane. This ion conductivity measurement cell is heated from about 25 ° C. (298K) to about 150 ° C. (423K) with a measurement time of about 5 minutes per point at a rate of about 5 ° C., and is manufactured by Solartron at a frequency of 0.1 Hz to 10 MHz.
- the ionic conductivity of the solid electrolyte membrane was measured using “SI-1260 impedance analyzer”.
- FIG. 2 shows the relationship between the ionic conductivity (1st) and the measurement temperature at this time.
- 7 Li-NMR was measured using a solid-state NMR apparatus (“CMX Infinity 300” manufactured by Chemicals) at a resonance frequency of 116 MHz and a temperature of 50 ° C. (323 K) to 260 ° C. (533 K). 7 Li-NMR longitudinal relaxation time was determined.
- FIG. 4A shows the 7 Li-NMR spectrum at each temperature.
- FIG. 5 shows the relationship between the 7 Li-NMR longitudinal relaxation time and the measurement temperature.
- An electrolyte membrane was prepared, and the ionic conductivity was measured while heating from about 20 ° C. (293 K) to about 150 ° C. (423 K) with a measurement time of about 5 minutes per point at about 5 ° C. increments.
- FIG. 3 shows the relationship between the ion conductivity and the measurement temperature. Table 1 shows the ionic conductivity at 77 ° C. (350 K).
- LiBH 4 manufactured by Aldrich, purity 90%
- FIG. 3 also shows the measurement results of the solid electrolyte membrane provided with LiI by Poulsen et al. (FW Poulsen et al., Solid State Ionics 9/10, 119 (1983)).
- Table 1 shows the ionic conductivity at 77 ° C. (350 K).
- Example 4 7 Li-NMR was measured for the solid electrolyte membrane under the conditions of a resonance frequency of 116 MHz and a temperature of 30 ° C. (303 K) to 260 ° C. (533 K) in the same manner as in Example 4, and the 7 Li-NMR longitudinal relaxation time was determined. Asked. FIG. 4B shows a 7 Li-NMR spectrum at each temperature. FIG. 5 shows the relationship between the 7 Li-NMR longitudinal relaxation time and the measurement temperature.
- the transition to the high temperature phase is less than the transition temperature (115 ° C.) of the high temperature phase of LiBH 4.
- the ionic conductivity decreased rapidly.
- the ionic conductivity is lower than that of LiBH 4 , and in particular, a high ionic conductivity was not obtained even at the transition temperature (115 ° C.) or higher.
- the solid electrolyte membrane of the present invention comprising LiBH 4 and LiI (Examples 4 to 5)
- the solid electrolyte membrane comprising only LiBH 4 above the transition temperature (115 ° C.)
- the ion conductivity was as high as that of the solid electrolyte membrane of Comparative Example 1 at a temperature lower than the transition temperature (115 ° C.). That is, by mixing LiI with LiBH 4 , it is preferable that heat treatment is performed to lower the transition temperature of the high-temperature phase compared to the case of LiBH 4 alone, and the ionic conductivity of LiI is low. It was confirmed that the ionic conductivity at a temperature lower than the transition temperature of the high temperature phase of LiBH 4 was increased, and a high ionic conductivity was obtained in a wider temperature range.
- the transition temperature (115 ° C.) is obtained by heating to the transition temperature (115 ° C.) or higher. It was confirmed that the ionic conductivity at less than 1 is increased. This is presumably because the crystallinity of the solid electrolyte was increased by heating, and the ratio of the high temperature phase was increased.
- LiBH 4 Aldrich, purity 90%
- LiI Aldrich, purity 99.999%)
- RbI Aldrich, purity 99.999%)
- the mixture was mixed at a molar ratio of .9: 0.1, and the mixture was press-molded (25 ° C., 100 MPa) to prepare pellets.
- the pellets were transferred to a glass cell, and then sintered by heating stepwise to 240 ° C. under vacuum. Thereafter, the sintered product was cooled to obtain a solid electrolyte.
- LiBH 4: LiI 3: also it shows the X-ray diffraction spectrum of the first solid electrolyte.
- a solid electrolyte membrane was prepared in the same manner as in Example 4, and the ionic conductivity was measured while heating from around 30 ° C. (303 K) to around 150 ° C. (423 K) in a measurement time of about 5 minutes per point at 5 ° C. .
- the relationship between the ionic conductivity and the measurement temperature at this time is shown in FIG.
- Example 4 7 Li-NMR was measured for the solid electrolyte membrane under the conditions of a resonance frequency of 116 MHz and a temperature of 50 ° C. (323 K) to 240 ° C. (513 K) in the same manner as in Example 4, and the 7 Li-NMR longitudinal relaxation time was determined. Asked.
- FIG. 8 shows the 7 Li-NMR spectrum at each temperature.
- FIG. 9 shows the relationship between the 7 Li-NMR longitudinal relaxation time and the measurement temperature.
- FIG. 9 also shows the results in Comparative Example 1.
- the transition temperature of the high-temperature phase is lowered and the ionic conductivity of LiI is low compared to the case of LiBH 4 alone. Nevertheless, a wide high ionic conductivity in the temperature range can be obtained, in particular, high ionic conductivity than LiBH 4 even above the transition temperature of the high-temperature phase of LiBH 4 could be obtained confirmed.
- the ionic conductivity was measured while heating from around 30 ° C. (303 K) to around 130 ° C. (403 K) with a measurement time of about 5 minutes per point at 10 ° C. increments. The relationship between the ionic conductivity and the measurement temperature at this time is shown in FIG.
- the ionic conductivity was measured while cooling from around 130 ° C. (403 K) to around 40 ° C. (313 K) with a measuring time of about 5 minutes per point at 10 ° C. increments.
- the relationship between the ionic conductivity and the measurement temperature at this time is shown in FIG.
- FIG. 10 the result in the comparative example 1 was also shown.
- the solid electrolyte membrane of the present invention comprising LiBH 4 , LiI, and CsI (Example 10) also has a comparison with the case of LiBH 4 alone (Comparative Example 1). Although the transition temperature of the high temperature phase is lowered and the ionic conductivity of LiI is low, the ionic conductivity is increased below the transition temperature of the high temperature phase of LiBH 4 , and a high ionic conductivity is obtained in a wider temperature range. It was confirmed.
- LiBH 4 manufactured by Aldrich, purity 90%
- LiNH 2 manufactured by Aldrich
- FIG. 11 shows the relationship between the ionic conductivity and the measurement temperature at this time.
- FIG. 11 shows the results of measurement for the solid electrolyte membrane comprising only LiBH 4 or only LiNH 2.
- the ionic conductivity was measured while heating from around 30 ° C. (303 K) to around 65 ° C. (338 K) in a measuring time of about 5 minutes per point.
- FIG. 11 shows the relationship between the ionic conductivity and the measurement temperature at this time.
- FIG. 11 shows the relationship between the ionic conductivity and the measurement temperature at this time.
- the transition temperature of the high-temperature phase decreases and the ionic conductivity of LiNH 2 is low
- the ionic conductivity is increased below the transition temperature of the high-temperature phase of LiBH 4
- high ionic conductivity is exhibited in a wider temperature range. It was confirmed that it was obtained.
- the solid electrolyte membrane and a LiBH 4 and LiNH 2 it tends to ionic conductivity when the content of LiNH 2 decreases becomes higher was confirmed.
- the solid electrolyte of the present invention exhibits high ionic conductivity even below the transition temperature (115 ° C.) of the high temperature phase of LiBH 4 , it is useful as a solid electrolyte for lithium ion secondary batteries.
Landscapes
- Chemical & Material Sciences (AREA)
- Manufacturing & Machinery (AREA)
- Engineering & Computer Science (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Electrochemistry (AREA)
- General Chemical & Material Sciences (AREA)
- Physics & Mathematics (AREA)
- General Physics & Mathematics (AREA)
- Condensed Matter Physics & Semiconductors (AREA)
- Inorganic Chemistry (AREA)
- Spectroscopy & Molecular Physics (AREA)
- Conductive Materials (AREA)
- Secondary Cells (AREA)
Abstract
Description
MX (1)
(式(1)中、Mはアルカリ金属原子を表し、Xは、ハロゲン原子、NR2基(Rは水素原子またはアルキル基を表す)およびN2R基(Rは水素原子またはアルキル基を表す)からなる群から選択される1種を表す。)で表されるアルカリ金属化合物とを備えるものである。前記LiBH4と前記アルカリ金属化合物とのモル比としてはLiBH4:アルカリ金属化合物=1:1~20:1が好ましい。このような固体電解質はリチウムイオン二次電池用固体電解質として有用である。
MX (1)
(式(1)中、Mはアルカリ金属原子を表し、Xは、ハロゲン原子、NR2基(Rは水素原子またはアルキル基を表す)およびN2R基(Rは水素原子またはアルキル基を表す)からなる群から選択される1種を表す。)
で表されるアルカリ金属化合物とを混合し、この混合物を加熱して溶融または焼結させ、その後、冷却することによって製造することができる。
MX (1)
(式(1)中、Mはアルカリ金属原子を表し、Xは、ハロゲン原子、NR2基(Rは水素原子またはアルキル基を表す)およびN2R基(Rは水素原子またはアルキル基を表す)からなる群から選択される1種を表す。)
で表されるアルカリ金属化合物とを備えるものである。
LiBH4(アルドリッチ社製、純度90%)とLiI(アルドリッチ社製、純度99.999%)とを、LiBH4:LiI=3:1のモル比で混合し、この混合物をガラスセルに移した後、320℃に加熱して溶融混合した。その後、この溶融混合物を室温まで冷却して固体電解質を得た。
LiBH4とLiIとのモル比をLiBH4:LiI=7:1に変更した以外は実施例1と同様にして固体電解質を調製した。この固体電解質(LiBH4:LiI=7:1)について実施例1と同様にしてX線回折測定を実施した。その結果を図1に示す。図1に示した結果から明らかなように、2θ=23.6deg、25.0deg、26.6deg、34.5deg、40.9deg、44.8degおよび48.6degの位置にX線回折ピークが観察された。
LiBH4とLiIとのモル比をLiBH4:LiI=15:1に変更した以外は実施例1と同様にして固体電解質を調製した。この固体電解質(LiBH4:LiI=15:1)について実施例1と同様にしてX線回折測定を実施した。その結果を図1に示す。図1に示した結果から明らかなように、2θ=23.8deg、24.8deg、26.9deg、34.6deg、40.7deg、44.8degおよび48.1degの位置にX線回折ピークが観察された。
実施例1と同様にして調製した溶融混合物(LiBH4:LiI=3:1)を円盤状(直径10mm、厚さ約2mm)にプレス成形(25℃、100MPa)して固体電解質膜を作製した。この固体電解質膜の両面に電極としてリチウム箔を装着してイオン伝導度測定セルを作製した。このイオン伝導度測定セルを約5℃刻みで1点につき5分程度の測定時間で25℃(298K)付近から150℃(423K)付近まで加熱しながら周波数0.1Hz~10MHzにおいてソーラートロン社製「SI-1260インピーダンスアナライザ」を用いて前記固体電解質膜のイオン伝導度を測定した。このときのイオン伝導度(1st)と測定温度との関係を図2に示す。
前記溶融混合物(LiBH4:LiI=3:1)の代わりに実施例2と同様にして調製した溶融混合物(LiBH4:LiI=7:1)を用いた以外は実施例4と同様にして固体電解質膜を作製し、約5℃刻みで1点につき5分程度の測定時間で20℃(293K)付近から150℃(423K)付近まで加熱しながらイオン伝導度を測定した。このイオン伝導度と測定温度との関係を図3に示す。また、77℃(350K)におけるイオン伝導度を表1に示す。
前記溶融混合物(LiBH4:LiI=3:1)の代わりにLiBH4(アルドリッチ社製、純度90%)を用いた以外は実施例4と同様にして固体電解質膜を作製し、約2.5℃刻みで1点につき5分程度の測定時間で60℃(333K)付近から160℃(433K)付近まで加熱しながらイオン伝導度を測定した。このときのイオン伝導度と測定温度との関係を図2および図3に示す。
LiBH4(アルドリッチ社製、純度90%)とLiI(アルドリッチ社製、純度99.999%)とRbI(アルドリッチ社製、純度99.999%)とを、LiBH4:LiI:RbI=3:0.9:0.1のモル比で混合し、この混合物をプレス成形(25℃、100MPa)してペレットを調製した。このペレットをガラスセルに移した後、真空下で240℃まで段階的に加熱して焼結させた。その後、この焼結物を冷却して固体電解質を得た。
LiBH4とLiIとRbIとのモル比をLiBH4:LiI:RbI=3:0.95:0.05に変更した以外は実施例6と同様にして固体電解質を調製した。この固体電解質(LiBH4:LiI:RbI=3:0.95:0.05)について実施例1と同様にしてX線回折測定を実施した。その結果を図6に示す。図6に示した結果から明らかなように、2θ=23.4deg、25.1deg、26.7deg、35.0degおよび41.5degの位置にX線回折ピークが観察された。また、LiBH4:LiI=3:1の固体電解質とは異なる回折ピーク(2θ=19.6deg、22.4deg、27.7deg、30.0degおよび35.9deg)も観察された。
LiBH4とLiIとRbIとのモル比をLiBH4:LiI:RbI=3:0.8:0.2に変更した以外は実施例6と同様にして固体電解質を調製した。この固体電解質(LiBH4:LiI:RbI=3:0.8:0.2)について実施例1と同様にしてX線回折測定を実施した。その結果を図6に示す。図6に示した結果から明らかなように、2θ=23.4deg、25.1deg、26.7deg、34.9degおよび41.4degの位置にX線回折ピークが観察された。また、LiBH4:LiI=3:1の固体電解質とは異なる回折ピーク(2θ=11.1deg、19.6deg、22.4deg、27.7deg、30.0degおよび35.9deg)も観察された。
前記溶融混合物(LiBH4:LiI=3:1)の代わりに実施例6と同様にして調製したペレット(LiBH4:LiI:RbI=3:0.9:0.1)を用いた以外は実施例4と同様にして固体電解質膜を作製し、5℃刻みで1点につき5分程度の測定時間で30℃(303K)付近から150℃(423K)付近まで加熱しながらイオン伝導度を測定した。このときのイオン伝導度と測定温度との関係を図7に示す。
RbIの代わりにCsI(アルドリッチ社製、純度99.999%)を用いた以外は実施例6と同様にしてペレット(LiBH4:LiI:CsI(モル比)=3:0.9:0.1)を調製した。前記ペレット(LiBH4:LiI:RbI)の代わりにこのペレット(LiBH4:LiI:CsI=3:0.9:0.1)を用いた以外は実施例9と同様にして固体電解質膜を作製し、10℃刻みで1点につき5分程度の測定時間で30℃(303K)付近から130℃(403K)付近まで加熱しながらイオン伝導度を測定した。このときのイオン伝導度と測定温度との関係を図10に示す。
LiBH4(アルドリッチ社製、純度90%)とLiNH2(アルドリッチ社製)とを、LiBH4:LiNH2=1:3のモル比で、遊星型ボールミルを用いてアルゴン雰囲気下で1時間混合した。この混合物をプレス成形(25℃、100MPa)した後、アルゴン雰囲気下、100℃で5時間加熱して焼結させて固体電解質膜を作製した。
LiBH4とLiNH2の混合モル比をLiBH4:LiNH2=1:1に変更し、加熱温度を60℃に変更した以外は実施例11と同様にして固体電解質を作製し、約10℃刻みで1点につき5分程度の測定時間で30℃(303K)付近から65℃(338K)付近まで加熱しながらイオン伝導度を測定した。このときのイオン伝導度と測定温度との関係を図11に示す。
Claims (12)
- LiBH4と、下記式(1):
MX (1)
(式(1)中、Mはアルカリ金属原子を表し、Xは、ハロゲン原子、NR2基(Rは水素原子またはアルキル基を表す)およびN2R基(Rは水素原子またはアルキル基を表す)からなる群から選択される1種を表す。)
で表されるアルカリ金属化合物とを備える固体電解質。 - 前記LiBH4と前記アルカリ金属化合物とのモル比がLiBH4:アルカリ金属化合物=1:1~20:1である、請求項1に記載の固体電解質。
- 115℃未満でのX線回折(CuKα:λ=1.5405Å)において、少なくとも、2θ=24.0±1.0deg、25.6±1.2deg、27.3±1.2deg、35.4±1.5deg、および42.2±2.0degの5箇所に回折ピークを有する請求項1に記載の固体電解質。
- 前記式(1)中のXがヨウ素原子およびアミノ基のうちのいずれか1種である、請求項1に記載の固体電解質。
- 前記アルカリ金属化合物がLiI、RbIおよびCsIからなる群から選択される少なくとも1種である、請求項4に記載の固体電解質。
- 請求項1に記載の固体電解質を備える二次電池。
- LiBH4と、下記式(1):
MX (1)
(式(1)中、Mはアルカリ金属原子を表し、Xは、ハロゲン原子、NR2基(Rは水素原子またはアルキル基を表す)およびN2R基(Rは水素原子またはアルキル基を表す)からなる群から選択される1種を表す。)
で表されるアルカリ金属化合物とを混合し、該混合物を加熱して溶融または焼結させ、その後、冷却する、固体電解質の製造方法。 - 前記混合物の加熱温度が50℃以上である、請求項7に記載の固体電解質の製造方法。
- 前記LiBH4と前記アルカリ金属化合物との混合モル比がLiBH4:アルカリ金属化合物=1:1~20:1である、請求項7に記載の固体電解質の製造方法。
- 前記式(1)中のXがヨウ素原子およびアミノ基のうちのいずれか1種である、請求項7に記載の固体電解質の製造方法。
- 前記アルカリ金属化合物がLiI、RbIおよびCsIからなる群から選択される少なくとも1種である、請求項10に記載の固体電解質の製造方法。
- 請求項7に記載の製造方法により得られた固体電解質を、115℃以上で加熱し、その後、冷却する、固体電解質の製造方法。
Priority Applications (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CN200980115518.7A CN102017269B (zh) | 2008-05-13 | 2009-05-12 | 固体电解质、其制造方法以及具备固体电解质的二次电池 |
US12/989,968 US9722276B2 (en) | 2008-05-13 | 2009-05-12 | Solid electrolyte, method for producing the same, and secondary battery comprising solid electrolyte |
KR1020107024335A KR101182972B1 (ko) | 2008-05-13 | 2009-05-12 | 고체 전해질, 그의 제조 방법 및 고체 전해질을 구비하는 이차 전지 |
JP2010511984A JP5187703B2 (ja) | 2008-05-13 | 2009-05-12 | 固体電解質、その製造方法、および固体電解質を備える二次電池 |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2008125862 | 2008-05-13 | ||
JP2008-125862 | 2008-05-13 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2009139382A1 true WO2009139382A1 (ja) | 2009-11-19 |
Family
ID=41318749
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2009/058835 WO2009139382A1 (ja) | 2008-05-13 | 2009-05-12 | 固体電解質、その製造方法、および固体電解質を備える二次電池 |
Country Status (5)
Country | Link |
---|---|
US (1) | US9722276B2 (ja) |
JP (1) | JP5187703B2 (ja) |
KR (1) | KR101182972B1 (ja) |
CN (2) | CN102017269B (ja) |
WO (1) | WO2009139382A1 (ja) |
Cited By (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20120251871A1 (en) * | 2011-03-29 | 2012-10-04 | Tohoku University | All-solid-state battery |
JP2012209104A (ja) * | 2011-03-29 | 2012-10-25 | Denso Corp | 全固体電池 |
JP2012209106A (ja) * | 2011-03-29 | 2012-10-25 | Denso Corp | 全固体電池 |
JP2015002156A (ja) * | 2013-06-18 | 2015-01-05 | 日本電信電話株式会社 | リチウム空気電池 |
WO2015030053A1 (ja) * | 2013-09-02 | 2015-03-05 | 三菱瓦斯化学株式会社 | 全固体電池および電極活物質の製造方法 |
WO2015030052A1 (ja) * | 2013-09-02 | 2015-03-05 | 三菱瓦斯化学株式会社 | 全固体電池 |
WO2016103894A1 (ja) * | 2014-12-22 | 2016-06-30 | 三菱瓦斯化学株式会社 | イオン伝導体およびその製造方法 |
WO2017126416A1 (ja) * | 2016-01-18 | 2017-07-27 | 三菱瓦斯化学株式会社 | イオン伝導体の製造方法 |
WO2017130674A1 (ja) * | 2016-01-27 | 2017-08-03 | 株式会社日立製作所 | 固定電解質および、固体電解質を用いた全固体リチウム電池 |
WO2018139629A1 (ja) * | 2017-01-30 | 2018-08-02 | 三菱瓦斯化学株式会社 | イオン伝導体及びその製造方法 |
JP2018170072A (ja) * | 2017-03-29 | 2018-11-01 | マクセルホールディングス株式会社 | 複合固体電解質、その製造方法、および全固体電池 |
RU2814874C1 (ru) * | 2020-02-17 | 2024-03-05 | Мицубиси Газ Кемикал Компани, Инк. | Ионный проводник, содержащий высокотемпературную фазу licb9h10, и способ его получения |
Families Citing this family (21)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US9312566B2 (en) | 2012-08-02 | 2016-04-12 | Toyota Motor Engineering & Manufacturing North America, Inc. | Magnesium borohydride and its derivatives as magnesium ion transfer media |
US9318775B2 (en) | 2012-08-02 | 2016-04-19 | Toyota Motor Engineering & Manufacturing North America, Inc. | Magnesium borohydride and its derivatives as magnesium ion transfer media |
US20140038037A1 (en) * | 2012-08-02 | 2014-02-06 | Toyota Motor Engineering & Manufacturing North America, Inc. | Magnesium borohydride and its derivatives as magnesium ion transfer media |
JP6759880B2 (ja) * | 2016-09-05 | 2020-09-23 | 三菱瓦斯化学株式会社 | イオン伝導体の製造方法 |
US10910672B2 (en) | 2016-11-28 | 2021-02-02 | Toyota Motor Engineering & Manufacturing North America, Inc. | High concentration electrolyte for magnesium battery having carboranyl magnesium salt in mixed ether solvent |
US10680280B2 (en) | 2017-09-26 | 2020-06-09 | Toyota Jidosha Kabushiki Kaisha | 3D magnesium battery and method of making the same |
CN108155411A (zh) * | 2017-12-05 | 2018-06-12 | 东南大学 | 一种硼氢化锂复合物快离子导体及其制备方法 |
CN108736064B (zh) * | 2018-07-11 | 2020-12-04 | 桑德新能源技术开发有限公司 | 一种复合硼氢化锂固态电解质及其制备方法和设备 |
CN109244535B (zh) * | 2018-11-01 | 2021-01-19 | 上海理工大学 | 硼氢化锂基固态电解质材料的制备方法 |
CN109585913B (zh) * | 2018-11-29 | 2021-08-24 | 东南大学 | 硼氢化锂与二硫化钼复合体系固态电解质材料及其制备方法和应用 |
CN112771627A (zh) * | 2018-12-26 | 2021-05-07 | 松下知识产权经营株式会社 | 卤化物的制造方法 |
AU2020231576A1 (en) | 2019-03-05 | 2021-09-09 | Mitsubishi Gas Chemical Company, Inc. | Method for producing sulfide solid electrolyte |
CN110380117B (zh) * | 2019-07-04 | 2020-12-08 | 光鼎铷业(广州)集团有限公司 | 一种铷掺杂的聚合物固态电解质膜的制备方法 |
RU2720349C1 (ru) * | 2019-11-11 | 2020-04-29 | Федеральное государственное бюджетное учреждение науки Институт химии твердого тела Уральского отделения Российской академии наук | Способ получения твердого электролита |
CN112259786B (zh) * | 2020-10-10 | 2022-07-12 | 南京航空航天大学 | 一种LiBH4-LiI-P2S5三元复合固态电解质及其制备方法 |
CN112331909A (zh) * | 2020-10-12 | 2021-02-05 | 南京航空航天大学 | 一种氨气掺杂硼氢化锂复合材料体系的锂离子导体及其制备方法 |
CN113097562B (zh) * | 2021-04-13 | 2024-04-05 | 无锡新锂耀辉能源科技有限公司 | 一种硼氢化锂-石榴石型氧化物复合固态电解质材料及其制备方法与应用 |
KR102655782B1 (ko) | 2021-06-03 | 2024-04-08 | 전남대학교산학협력단 | 이차전지용 전해질 및 이를 포함하는 이차전지 |
CN113991171B (zh) * | 2021-10-22 | 2023-03-24 | 浙江大学 | 一种石榴石型多元复合固态电解质及其制备方法和应用 |
CN114421002A (zh) * | 2022-01-04 | 2022-04-29 | 浙江大学 | 石榴石氧化物/配位硼氮氢化物复合的固态电解质及其制备方法和应用 |
KR20230174555A (ko) | 2022-06-21 | 2023-12-28 | 전남대학교산학협력단 | 리튬 이차전지용 전해질 및 이를 포함하는 리튬 이차전지 |
Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2000123874A (ja) * | 1998-10-16 | 2000-04-28 | Matsushita Electric Ind Co Ltd | 固体電解質成型体、電極成型体および電気化学素子 |
JP2003077462A (ja) * | 2001-09-03 | 2003-03-14 | Japan Storage Battery Co Ltd | 非水電解質二次電池 |
Family Cites Families (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US6022637A (en) * | 1984-10-23 | 2000-02-08 | Wilson; John T. R. | High temperature battery |
JP3163741B2 (ja) * | 1992-05-08 | 2001-05-08 | 松下電器産業株式会社 | 非晶質リチウムイオン導電性固体電解質およびその製造方法 |
US5731117A (en) * | 1995-11-06 | 1998-03-24 | Eastman Kodak Company | Overcoated charge transporting elements and glassy solid electrolytes |
JPH11185811A (ja) * | 1997-12-16 | 1999-07-09 | Tonen Corp | リチウム電池用電解液及びその製造方法 |
TW408508B (en) * | 1997-12-26 | 2000-10-11 | Tonen Corp | An electrolytic solution for a lithium battery and a process for preparing the same |
JP4361229B2 (ja) * | 2001-07-04 | 2009-11-11 | 日産自動車株式会社 | 電池システム |
JP4813767B2 (ja) | 2004-02-12 | 2011-11-09 | 出光興産株式会社 | リチウムイオン伝導性硫化物系結晶化ガラス及びその製造方法 |
JP4834442B2 (ja) | 2006-03-31 | 2011-12-14 | 出光興産株式会社 | 固体電解質、その製造方法及び全固体二次電池 |
-
2009
- 2009-05-12 WO PCT/JP2009/058835 patent/WO2009139382A1/ja active Application Filing
- 2009-05-12 CN CN200980115518.7A patent/CN102017269B/zh active Active
- 2009-05-12 US US12/989,968 patent/US9722276B2/en active Active
- 2009-05-12 KR KR1020107024335A patent/KR101182972B1/ko active IP Right Grant
- 2009-05-12 CN CN201310502796.6A patent/CN103606712B/zh active Active
- 2009-05-12 JP JP2010511984A patent/JP5187703B2/ja active Active
Patent Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2000123874A (ja) * | 1998-10-16 | 2000-04-28 | Matsushita Electric Ind Co Ltd | 固体電解質成型体、電極成型体および電気化学素子 |
JP2003077462A (ja) * | 2001-09-03 | 2003-03-14 | Japan Storage Battery Co Ltd | 非水電解質二次電池 |
Non-Patent Citations (2)
Title |
---|
HIDEKI MAEKAWA ET AL.: "Halide-Stabilized LiBH4, a Room-Temperature Lithium Fast-Ion Conductor", JOURNAL OF THE AMERICAN CHEMICAL SOCIETY, vol. 131, 2 January 2009 (2009-01-02), pages 894 - 895 * |
MOTOAKI MATSUO ET AL.: "LiBH4 ni Okeru Li Cho Ion Dendo", ABSTRACTS OF THE JAPAN INSTITUTE OF METALS, 2008 NEN SHUNKI DAI 142 KAI TAIKAI, THE JAPAN INSTITUTE OF METALS, 26 March 2008 (2008-03-26), pages 171 * |
Cited By (25)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2012209104A (ja) * | 2011-03-29 | 2012-10-25 | Denso Corp | 全固体電池 |
JP2012209106A (ja) * | 2011-03-29 | 2012-10-25 | Denso Corp | 全固体電池 |
US20120251871A1 (en) * | 2011-03-29 | 2012-10-04 | Tohoku University | All-solid-state battery |
JP2015002156A (ja) * | 2013-06-18 | 2015-01-05 | 日本電信電話株式会社 | リチウム空気電池 |
US10038192B2 (en) | 2013-09-02 | 2018-07-31 | Mitsubishi Gas Chemical Company, Inc. | Solid-state battery |
WO2015030053A1 (ja) * | 2013-09-02 | 2015-03-05 | 三菱瓦斯化学株式会社 | 全固体電池および電極活物質の製造方法 |
WO2015030052A1 (ja) * | 2013-09-02 | 2015-03-05 | 三菱瓦斯化学株式会社 | 全固体電池 |
JPWO2015030052A1 (ja) * | 2013-09-02 | 2017-03-02 | 三菱瓦斯化学株式会社 | 全固体電池 |
JPWO2015030053A1 (ja) * | 2013-09-02 | 2017-03-02 | 三菱瓦斯化学株式会社 | 全固体電池および電極活物質の製造方法 |
US10147937B2 (en) | 2013-09-02 | 2018-12-04 | Mitsubishi Gas Chemical Company, Inc. | Solid-state battery and method for manufacturing electrode active material |
WO2016103894A1 (ja) * | 2014-12-22 | 2016-06-30 | 三菱瓦斯化学株式会社 | イオン伝導体およびその製造方法 |
US10411295B2 (en) | 2014-12-22 | 2019-09-10 | Mitsubishi Gas Chemical Company, Inc. | Ionic conductor and method for producing the same |
JPWO2016103894A1 (ja) * | 2014-12-22 | 2017-09-28 | 三菱瓦斯化学株式会社 | イオン伝導体およびその製造方法 |
KR102355583B1 (ko) | 2014-12-22 | 2022-01-25 | 미츠비시 가스 가가쿠 가부시키가이샤 | 이온 전도체 및 그의 제조 방법 |
KR20170097671A (ko) * | 2014-12-22 | 2017-08-28 | 미츠비시 가스 가가쿠 가부시키가이샤 | 이온 전도체 및 그의 제조 방법 |
US10825574B2 (en) | 2016-01-18 | 2020-11-03 | Mitsubishi Gas Chemical Company, Inc. | Method for manufacturing ionic conductor |
JPWO2017126416A1 (ja) * | 2016-01-18 | 2018-11-15 | 三菱瓦斯化学株式会社 | イオン伝導体の製造方法 |
WO2017126416A1 (ja) * | 2016-01-18 | 2017-07-27 | 三菱瓦斯化学株式会社 | イオン伝導体の製造方法 |
CN108475565A (zh) * | 2016-01-18 | 2018-08-31 | 三菱瓦斯化学株式会社 | 离子传导体的制造方法 |
CN108475565B (zh) * | 2016-01-18 | 2020-11-06 | 三菱瓦斯化学株式会社 | 离子传导体的制造方法 |
WO2017130674A1 (ja) * | 2016-01-27 | 2017-08-03 | 株式会社日立製作所 | 固定電解質および、固体電解質を用いた全固体リチウム電池 |
WO2018139629A1 (ja) * | 2017-01-30 | 2018-08-02 | 三菱瓦斯化学株式会社 | イオン伝導体及びその製造方法 |
JP2018170072A (ja) * | 2017-03-29 | 2018-11-01 | マクセルホールディングス株式会社 | 複合固体電解質、その製造方法、および全固体電池 |
JP7008420B2 (ja) | 2017-03-29 | 2022-01-25 | マクセル株式会社 | 複合固体電解質、その製造方法、および全固体電池 |
RU2814874C1 (ru) * | 2020-02-17 | 2024-03-05 | Мицубиси Газ Кемикал Компани, Инк. | Ионный проводник, содержащий высокотемпературную фазу licb9h10, и способ его получения |
Also Published As
Publication number | Publication date |
---|---|
US20110117440A1 (en) | 2011-05-19 |
JP5187703B2 (ja) | 2013-04-24 |
KR20100139116A (ko) | 2010-12-31 |
CN103606712B (zh) | 2016-01-20 |
CN102017269A (zh) | 2011-04-13 |
KR101182972B1 (ko) | 2012-09-18 |
CN102017269B (zh) | 2015-09-30 |
US9722276B2 (en) | 2017-08-01 |
JPWO2009139382A1 (ja) | 2011-09-22 |
CN103606712A (zh) | 2014-02-26 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP5187703B2 (ja) | 固体電解質、その製造方法、および固体電解質を備える二次電池 | |
Wang et al. | The prospect and challenges of sodium‐ion batteries for low‐temperature conditions | |
Liu et al. | Spinel LiNi 0.5 Mn 1.5 O 4 and its derivatives as cathodes for high-voltage Li-ion batteries | |
TW200529247A (en) | Lithium ion conducting sulfide based crystallized glass and method for production thereof | |
TWI712197B (zh) | 離子傳導體之製造方法 | |
JP7141635B2 (ja) | リチウムイオン伝導性ポリマー電解質 | |
CN113258130B (zh) | 非晶卤化物固体电解质及制备和在全固态电池中的应用 | |
KR101816289B1 (ko) | 고체 전해질의 제조 방법, 상기 제조 방법에 의해 제조된 고체 전해질, 및 상기 고체 전해질을 포함하는 전고체 전지 | |
Aravindan et al. | Li+ ion conduction in TiO2 filled polyvinylidenefluoride-co-hexafluoropropylene based novel nanocomposite polymer electrolyte membranes with LiDFOB | |
JP2021118030A (ja) | 硫化物系固体電解質の製造方法 | |
Yang et al. | Inorganic All‐Solid‐State Sodium Batteries: Electrolyte Designing and Interface Engineering | |
Jia et al. | Li–Solid Electrolyte Interfaces/Interphases in All-Solid-State Li Batteries | |
US11063293B2 (en) | Increasing ionic conductivity of LiTi2(PS4)3 by Zr doping | |
JP4568619B2 (ja) | イオン伝導体 | |
US10807877B2 (en) | Increasing ionic conductivity of LiTi2(PS4)3 by Al doping | |
JP7022498B2 (ja) | イオン伝導体の経時劣化を抑制する方法 | |
KR102393999B1 (ko) | 고체 리튬 전지용 황계 고체전해질 및 고체전해질의 상압 합성법 | |
Shindrov et al. | Solvent free PEO-NaClO4: Na3Zr2Si2PO12 composite solid polymer electrolytes: Comparison of conductive properties of “ceramics-in-polymer” and “polymer-in-ceramics” | |
Vineeth et al. | Electrolytes for room-temperature sodium-sulfur batteries: A holistic approach to understand solvation | |
JP4515936B2 (ja) | イオン伝導体 | |
CN114497713B (zh) | 一种含氟固态电解质及其制备方法与应用 | |
Nangir et al. | Super Ionic Li3–2xMx (OH) 1-yNyCl (M= Ca, W, N= F) Halide Hydroxide as an Anti-Perovskite Electrolyte for Solid-State Batteries | |
CN116960445A (zh) | Li-B-S体系硫化物固态电解质及其制备方法和电池 | |
Gao et al. | Enhancing Ionic Conductivity and Electrochemical Stability of Li3PS4 via Zn, F Co-Doping for All-Solid-State Li–S Batteries | |
KR20240078960A (ko) | 세라믹 고체 전해질의 제조 방법 및 이에 따라 제조된 세라믹 고체 전해질 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
WWE | Wipo information: entry into national phase |
Ref document number: 200980115518.7 Country of ref document: CN |
|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 09746588 Country of ref document: EP Kind code of ref document: A1 |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2010511984 Country of ref document: JP |
|
ENP | Entry into the national phase |
Ref document number: 20107024335 Country of ref document: KR Kind code of ref document: A |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
WWE | Wipo information: entry into national phase |
Ref document number: 12989968 Country of ref document: US |
|
122 | Ep: pct application non-entry in european phase |
Ref document number: 09746588 Country of ref document: EP Kind code of ref document: A1 |