CN1937299A - Lithium-lanthanum-silicon-sulfur solid electrolyte material for secondary lithium cell and its preparing method - Google Patents
Lithium-lanthanum-silicon-sulfur solid electrolyte material for secondary lithium cell and its preparing method Download PDFInfo
- Publication number
- CN1937299A CN1937299A CNA2006101168132A CN200610116813A CN1937299A CN 1937299 A CN1937299 A CN 1937299A CN A2006101168132 A CNA2006101168132 A CN A2006101168132A CN 200610116813 A CN200610116813 A CN 200610116813A CN 1937299 A CN1937299 A CN 1937299A
- Authority
- CN
- China
- Prior art keywords
- solid electrolyte
- powder
- lanthanum
- electrolyte material
- lithium
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Images
Classifications
-
- 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
Landscapes
- Conductive Materials (AREA)
- Secondary Cells (AREA)
Abstract
Characters of the invention are that chemical composition of solid electrolyte of Li-La-Si-S is compound from three different sulfides Li2S, La2S3 and SiS2 according to mol ratio 6 : 0.5 : 3. The solid electrolyte forms system of amorphous state to provide transmission space for lithium ion so as to obtain higher ionic conductivity (ionic conductivity in room temperature about 5.35*10-5S/cm), and lower electron conductivity (electron conductivity in room temperature<1.0*10-8S/cm=, lower activation energy of material (0.129eV), and wider thermostable range (room temperature - 200 deg.C). The invention provides comparative ideal candidate of electrolyte material for practical lithium ion battery in full solid state.
Description
Technical field
The present invention relates to a kind of brand-new sulfide system Li that can be used for the serondary lithium battery solid electrolyte material
2S-La
2S
3-SiS
2And preparation method thereof.This material system (≤200 ℃) under room temperature and higher temperature mainly shows as lithium ion conductor, and its room temperature total conductivity can reach 5.35 * 10
-5S/cm, its activation energy only are 0.129eV, far below the sulfide system of present report, belong to energy and material.
Background technology
Be accompanied by extensive uses such as portable electronics such as mobile phone, video camera and notebook computer, lithium ion two battery eliminators are well received.These batteries have high output voltage, high energy storage density and carry light advantage.The most employed electrolyte of lithium battery comprises volatile and incendive organic solvent at present.In order to make more high output voltage, the more high-energy-density and the battery of large scale more, just need to use the electrolyte that contains a large amount of organic solvents.And the organic bath in the battery causes serious fire and electrolyte leakage to happen occasionally.Overcome these safety problems and produce reliable battery, effective method is exactly to replace inflammable liquid electrolyte with the solid electrolyte that does not fire.In order to guarantee the high-performance of solid lithium battery, solid electrolyte must have the high-lithium ion conductance similar with liquid electrolyte.The research of current solid electrolyte concentrates on the novel porous material of taking or be construction unit with organic substance as the leading factor.And pure inorganic system never causes some important researchs are arranged concern widely recently.
Main at present research concentrates on the material relevant with oxide mostly with the inorganic solid electrolyte of using (fast-ionic conductor).This class material has bigger ion activation energy usually, and just its ionic conductivity is higher when high temperature (＞100 ℃), but very low when the room temperature left and right sides.Discover that in a large number the oxide with open architecture can improve the cationic electroconductive under the normal temperature because open passage for the ion migration provides may.In order to improve the cationic mobility of conduction, the oxide fast-ionic conductor generally adopts amorphous batch mixing or glass physics attitude, this decrystallized structure makes material internal have more defectives, bigger sponginess and high-energy more, promptly improve the openness of its structure, reduce oxonium ion to cationic binding force, thereby improve cationic transfer ability.However, the oxonium ion (O on oxide holes frame surface
2-) to the conduction cation (Li in the passage
+And Na
+) still have very strong charge effect, cause these to conduct electricity cationic migration and be subjected to very big constraint.
Compare with oxide, the chalcogenide of open architecture then is more suitable for as fast-ionic conductor.The sulfur family atomic electronegativity does not have oxygen strong, sulfur family ion (Q
2-) on CHARGE DISTRIBUTION compare O
2-Delocalizationization more, the just easier polarization of the sulfur family ion on frame surface, hole, so chalcogenide is more suitable for cationic migration.Such as, at normal temperatures, sulfide 0.6Li
2S: 0.4SiS
2The conductance of (mol ratio) reaches 10
-3The S/cm order of magnitude, and corresponding oxide 0.6Li
2O: 0.4SiO
2Conductance have only 10
-6The S/cm order of magnitude [1-3] [(1) Yamamoto H, Machida N, et.al.Solid State Ionics 175 (1-4): 707-711,2004. (2) Hayashi A, Araki R, et.al.Solid State Ionics 113-115,733,1998. (3) Zheng N, Bu X, Feng P, Nature 426,428,2003.].This shows that chalcogenide has very big advantage as fast-ionic conductor.
Sulfide amorphous batch mixing or glass are focuses as the research of fast-ionic conductor at present.Their method mainly is Li
2S and sulfide M S
2(M=Si, Ge), P
2S
5Deng in one or more mixing, by ball milling, high-energy ball milling or fuse and obtain.The sulfide crystallization shape material of open architecture also is one of optimal candidate of fast-ionic conductor.Delivered the synthetic loose structure that contains of the inorganic sulfur compounds of group fast-ionic conductor of crystallization in November, 2003 in Britain's " nature ", wherein contain Li
+Or Na
+CuINS-Na in the literary composition (ICF-5) and InSe-Na (ICF-21) conductance at normal temperatures are respectively 1.2H10
-2And 3.4H10
-2S/cm.Show that thus the crystalline state material can have the conductance that is higher than or is similar to glassy state.
From the practical application angle, all-solid lithium battery is compared with traditional liquid electrolyte battery, except higher energy is arranged, also avoided the corrosion of liquid electrolytic confrontation containers such as soda acid, and have do not have to reveal, storage life is long, be easy to advantage such as miniaturization, and the serviceability temperature scope is extensive especially, makes the range of application of lithium battery expand to space flight, the operational environment of multiple specific (special) requirements such as biology and human body, it will more and more influence and change people's life.
In sum, the search research and development utilization that is used for the solid electrolyte material of serondary lithium battery is of great immediate significance.
Summary of the invention
The object of the present invention is to provide a kind of lithium-lanthanum-silicon-sulfur solid electrolyte material that is used for serondary lithium battery and preparation method thereof, being contemplated that of invention: the sulfide of open architecture can have good cationic electroconductive and chemical stability, is expected to become the most promising fast-ionic conductor after oxide.In order to guarantee that sulfide can have the skeleton of negative electrical charge, M
N+The ratio of/S is the smaller the better, and just the valence state of M is high more good more, as the valence state n of M can be+3 ,+4 ,+5 ,+6.Be that M is early transition metal (the 3rd, 4,5 family) or back metallic element (the 13rd, 14,15 family) and rare earth element.These materials have the abundant structures type, from three-dimensional to two dimension, one dimension or zero-dimension structural.Lithium ion is arranged between duct, interlayer, interchain or point, and its coordination mode is various.Coordination mode as lithium ion and sulfur family ion can be coordinated to 5,4 coordinations from 6.Represent material as, LiLnS
2(Ln is a rare earth element), Na
5Li
3Ti
2S
8, NaLiMS
2(M=Zn, Cd) etc., but the lithium ion transmission performance of these materials is not also by systematic research.We are by research Li
2S-La
2S
3Compound with other sulfide, find that this sulfide system compares with the present oxide solid electrolyte of main flow, its sulphion is because radius is bigger, compare with oxonium ion, easier polarization is more suitable for the lithium ion diffusion, thereby obtains higher lithium ion conductivity.In experiment, we find Li
2S-La
2S
3Though system at room temperature has higher ionic conductivity, this system undergoes phase transition in the time of 80 ℃, causes its conductivity to reduce three orders of magnitude rapidly.In order to obtain that higher ionic conductivity is arranged in bigger temperature window, we adopt Li
2S-La
2S
3With SiS
2, P
2S
5Sulfides is compound.
In the present invention, we select Li
2S-La
2S
3-SiS
2Non-crystalline material is as research system.This is that mainly its structure is an amorphous state, material internal has more defectives, bigger sponginess and high-energy more, promptly improve the openness of its structure, reduce anion to cationic binding force, thereby improve cationic transfer ability, and then can obtain higher ionic conductivity and lower ion activation energy.The Li that in experiment, prepares by the test distinct methods
2S-La
2S
3-SiS
2System, this system under room temperature and higher temperature (≤200 ℃) mainly show as lithium ion conductor, and room temperature total conductivity is the highest can reach 5.35 * 10 for it
-5S/cm, and have lower activation energy (0.129eV), the lithium ion sulfide fast-ionic conductor that only is report at present is (about half of 0.3～0.5eV).Up to the present, as yet not relevant for Li
2S, La
2S
3And SiS
2The related content report of compound system.Compare Li with the lithium ion sulfide system of having reported
2S-La
2S
3-SiS
2The system conductivity is lower, also needs the composition and the preparation technology of this system are done further improvement.
We adopt traditional solid-phase sintering and these two kinds of diverse ways of high-energy ball milling to prepare powder body material.Raw material adopts commercially available sublimed sulfur (99%), lanthanum powder (99.99%), silica flour (99%, 200 order) and Li
2S, SiS
2And La
2S
3Purity 〉=99.0%.
Embodiment of the present invention is as follows:
1, material preparation
Scheme one,
With Li
2S, La
2S
3And SiS
2Powder was by 6: 0.5: 3 mixed in molar ratio, and high-energy ball milling jar (ZrO packs into
2Material) in, high-energy ball milling is 10 hours under the argon gas atmosphere protection, and compressing tablet (diameter 10mm, thickness 1mm, pressure are 5-10MPa) is finally made lithium ion fast-ionic conductor test material.
Scheme two,
Select Li for use
2S, SiS
2And La
2S
3Powder (the Li of perhaps an amount of mol ratio
2S, La powder, S powder and Si powder) according to Li
2S: La
2S
3: SiS
2=6: (mol ratio) mixed was prepared burden in 0.5: 3, the quartz glass tube of packing into then, and encapsulation is carried out solid phase reaction at 650 ℃～750 ℃ after vacuumizing, and the reaction time is 10～12 hours.The solid phase reaction second time was carried out in encapsulation again after powder ground behind the open pipe, and condition and preceding similar is taken out at high temperature at last, and quenching is to room temperature.The material that obtains is ground, and the compressing tablet process is identical with scheme one.
Scheme three,
Select Li for use
2S, SiS
2And La
2S
3Powder (the Li of perhaps an amount of mol ratio
2S, La powder, S powder and Si powder) according to Li
2S: La
2S
3: SiS
2=6: (mol ratio) mixed was prepared burden in 0.5: 3, the quartz glass tube of packing into then, and encapsulation is carried out solid phase reaction at 650 ℃～750 ℃ after vacuumizing, and the reaction time is 10～12 hours.The solid phase reaction second time was carried out in encapsulation again after powder ground behind the open pipe, and condition and preceding similar slowly cools to room temperature at last.The material that obtains is ground, and the compressing tablet process is identical with scheme one.
Batch mixing in the scheme 2 and 3 and grind all behind the solid phase reaction open pipe for the first time and under the argon atmospher protection, carry out, and solid phase reaction not only only limits to secondary, and more times increases cost.The described degree of exhaustion that vacuumizes encapsulation is lower than 10
-2Pa, encapsulation is adopting quartz glass oxyhydrogen flame sealing by fusing commonly used just.
2, performance evaluation (electric property)
The indium film that gained sample of the present invention two sides compacting one deck is thin carries out the electric conductivity evaluation as conductive electrode on electrochemical workstation (Shanghai occasion China 660B).
Description of drawings
Fig. 1 6Li
2S-0.5La
2S
3-3SiS
2The alternating temperature impedance spectrum
Fig. 2 6Li
2S-0.5La
2S
3-3SiS
2Conductivity varies with temperature curve
Fig. 3 6Li
2S-0.5La
2S
3-3SiS
2The product of conductivity and temperature varies with temperature curve
Embodiment
Introduce embodiments of the invention below, but the present invention is limited to embodiment absolutely not.
Embodiment 1:
Adopt Li
2S and SiS
2And La
2S
3Powder (purity is respectively 99%, 99.0%, 99.0%)) according to 6: 0.5: 3 the molar ratio weighings and the high-energy ball milling jar (ZrO that packs into
2Material) in, high-energy ball milling is 10 hours under the argon gas atmosphere protection, and last compressing tablet (diameter 10mm, thickness 1mm, pressure are 8MPa) as conductive electrode, is finally made the block test material of solid electrolyte at surface compacting one deck indium film.
Conducting performance test shows that it has the ionic conductance performance, and the low frequency end of the ac impedance spectroscopy under different temperatures can clearly observe the peculiar straightway of ionic conductivity.By calculating, can obtain its room temperature total conductivity is 5.35 * 10
-5S/cm simultaneously, is mapped to 1000/T by lg σ T, and the ion transfer activation energy that obtains this material is (0.129eV).
Embodiment 2:
Adopt Li
2S, SiS
2And La
2S
3Powder (purity is respectively 99%, 99.0%, 99.0%) vacuumizes (less than 10 according to 6: 0.5: 3 the molar ratio weighings and the glass tube of packing into
-2Pa) the oxyhydrogen flame sealing by fusing is used in the back, and the glass tube that mixture is housed slowly is warming up to 450 ℃ and be incubated 24h, is warming up to 650 ℃～750 ℃ then and carries out solid phase reaction, and the reaction time is 10～12h.Open pipe behind the water-cooled quenching, powder grinds under the argon gas atmosphere protection, and the compressing tablet process is identical with test implementation mode 1.
The performance test results and 1 basic identical, its conductivity at room temperature is 1.25 * 10
-5S/cm is lower than embodiment 1.
Embodiment 3:
Adopt La powder, Si powder, S powder and Li
2S powder (purity is respectively 99.99%, 99.9%, 99% and 99.0%) is according to 6Li
2S-0.5La
2S
3-3SiS
2The stoichiometric proportion weighing and the glass tube of packing into, the method for pressing execution mode 2 is finally made solid electrolyte material.
The performance test results and 1 basic identical, its room temperature electricity is led about rate 1.0 * 10
-5S/cm is lower than embodiment 1 and 2.
Embodiment 4:
Adopt La powder, Si powder, S powder and Li
2S powder (purity is respectively 99.99%, 99.9%, 99% and 99.0%) is finally made the block materials of solid electrolyte according to embodiment three.
The conductivity test result shows that its conductivity at room temperature rate will be far below embodiment 1,2 and 3, and its ionic conductivity is greatly about 10
-7About S/cm.
Claims (10)
1, a kind of lithium-lanthanum-silicon-sulfur solid electrolyte material that is used for serondary lithium battery is characterized in that described solid electrolyte material is Li
2S, La
2S
3And SiS
2Three kinds of different sulfide are compound by 6: 0.5: 3 mol ratio.
2, by the described lithium-lanthanum-silicon-sulfur solid electrolyte material that is used for serondary lithium battery of claim 1, it is characterized in that described solid electrolyte material forms amorphous state, lithium ion is diffused in wherein.
3, the preparation method that is used for the lithium-lanthanum-silicon-sulfur solid electrolyte material of serondary lithium battery as claimed in claim 1 is characterized in that selecting in following three kinds of methods any one:
A. with Li
2S, La
2S
3And SiS
2Powder is by 6: 0.5: 3 mixed in molar ratio, in the high-energy ball milling jar of packing into, and under the argon gas atmosphere protection high-energy ball milling 8-12 hour, dry pressing then;
B. select Li for use
2S, La
2S
3And SiS
2Powder or Li
2S, La powder, S powder and Si powder are Li in molar ratio
2S: La
2S
3: SiS
2=6: mixing in 0.5: 3 is prepared burden, the quartz glass tube of packing into then, encapsulation after vacuumizing, carry out solid phase reaction at 650 ℃～750 ℃, the solid phase reaction second time was carried out in encapsulation again after powder ground behind the open pipe, condition is taken out at high temperature at last with for the first time identical, and quenching is to room temperature.With material grinding, the dry pressing that obtains;
C. select Li for use
2S, La
2S
3And SiS
2Powder or Li
2S, the La powder, S powder and Si powder are Li in molar ratio
2S: La
2S
3: SiS
2=6: mixing in 0.5: 3 is prepared burden, the quartz glass tube of packing into then, encapsulation after vacuumizing, carry out solid phase reaction at 650 ℃～750 ℃, the solid phase reaction second time was carried out in encapsulation again after powder ground behind the open pipe, condition and preceding similar slowly cools to room temperature at last.With material grinding, the dry pressing that obtains;
Batch mixing in B and the C method and for the first time after the solid phase reaction open pipe grind all and under argon atmospher, carry out.
4,, it is characterized in that the abrading-ball that the high-energy ball milling jar uses is ZrO by the described preparation method who is used for the lithium-lanthanum-silicon-sulfur solid electrolyte material of serondary lithium battery of claim 3
2Ball.
5,, it is characterized in that the vacuum degree that vacuumizes sealing by fusing is lower than 10 by the described preparation method who is used for the lithium-lanthanum-silicon-sulfur solid electrolyte material of serondary lithium battery of claim 3
-2Pa.
6, by the described preparation method who is used for the lithium-lanthanum-silicon-sulfur solid electrolyte material of serondary lithium battery of claim 3, it is characterized in that quartz glass tube oxyhydrogen flame sealing by fusing.
7,, it is characterized in that the solid phase reaction time is 10-12 hour by the described preparation method who is used for the lithium-lanthanum-silicon-sulfur solid electrolyte material of serondary lithium battery of claim 3.
8,, it is characterized in that described solid phase reaction is not only limited to secondary by the described preparation method who is used for the lithium-lanthanum-silicon-sulfur solid electrolyte material of serondary lithium battery of claim 3.
9, by the described preparation method who is used for the lithium-lanthanum-silicon-sulfur solid electrolyte material of serondary lithium battery of claim 3, it is characterized in that sublimed sulfur＞99%, the lanthanum powder purity used are 99.99%, silica flour purity is 99%; Li
2S, La
2S
3And SiS
2Purity is 〉=99.0%.
10, by the described method that is used for the lithium-lanthanum-silicon-sulfur solid electrolyte material of serondary lithium battery of claim 3, the pressure when it is characterized in that dry pressing is 5-10MPa.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2006101168132A CN100486024C (en) | 2006-09-29 | 2006-09-29 | Lithium-lanthanum-silicon-sulfur solid electrolyte material for secondary lithium cell and its preparing method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2006101168132A CN100486024C (en) | 2006-09-29 | 2006-09-29 | Lithium-lanthanum-silicon-sulfur solid electrolyte material for secondary lithium cell and its preparing method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1937299A true CN1937299A (en) | 2007-03-28 |
| CN100486024C CN100486024C (en) | 2009-05-06 |
Family
ID=37954667
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB2006101168132A Active CN100486024C (en) | 2006-09-29 | 2006-09-29 | Lithium-lanthanum-silicon-sulfur solid electrolyte material for secondary lithium cell and its preparing method |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN100486024C (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101971408A (en) * | 2008-07-25 | 2011-02-09 | 丰田自动车株式会社 | Li-la-ti-o composite solid electrolyte material containing silicon and synthesizing method thereof |
| CN105098228A (en) * | 2014-05-05 | 2015-11-25 | 中国科学院宁波材料技术与工程研究所 | Sulfide solid electrolyte material and preparation method thereof |
| CN106785021A (en) * | 2017-02-13 | 2017-05-31 | 桂林电器科学研究院有限公司 | A kind of lithium sulfide system solid electrolyte material for adding Li-Si alloy, silver iodide and silver chlorate and preparation method thereof |
| CN108886175A (en) * | 2016-03-28 | 2018-11-23 | 巴斯夫公司 | Silicon substrate solid electrolyte for rechargeable batteries |
| CN109761265A (en) * | 2019-01-23 | 2019-05-17 | 宁德新能源科技有限公司 | Solid electrolyte and preparation method thereof with include its electrochemical appliance and electronic device |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1006943B (en) * | 1985-05-23 | 1990-02-21 | 南京航空学院 | Solid electrolyte hectorite and application thereof in battery |
| EP1675206B1 (en) * | 2003-06-27 | 2012-08-08 | Panasonic Corporation | Solid-state electrolyte and all solid-state battery using same electrolyte |
| US20070248888A1 (en) * | 2004-06-04 | 2007-10-25 | Idemitsu Kosan Co., Ltd. | High-Performance All-Solid Lithium Battery |
-
2006
- 2006-09-29 CN CNB2006101168132A patent/CN100486024C/en active Active
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101971408A (en) * | 2008-07-25 | 2011-02-09 | 丰田自动车株式会社 | Li-la-ti-o composite solid electrolyte material containing silicon and synthesizing method thereof |
| CN101971408B (en) * | 2008-07-25 | 2016-04-27 | 丰田自动车株式会社 | Siliceous Li-La-Ti oxygen composite solid electrolyte material and preparation method thereof |
| CN105098228A (en) * | 2014-05-05 | 2015-11-25 | 中国科学院宁波材料技术与工程研究所 | Sulfide solid electrolyte material and preparation method thereof |
| CN108886175A (en) * | 2016-03-28 | 2018-11-23 | 巴斯夫公司 | Silicon substrate solid electrolyte for rechargeable batteries |
| CN108886175B (en) * | 2016-03-28 | 2022-08-02 | 巴斯夫公司 | Silicon-based solid electrolyte for rechargeable batteries |
| CN106785021A (en) * | 2017-02-13 | 2017-05-31 | 桂林电器科学研究院有限公司 | A kind of lithium sulfide system solid electrolyte material for adding Li-Si alloy, silver iodide and silver chlorate and preparation method thereof |
| CN109761265A (en) * | 2019-01-23 | 2019-05-17 | 宁德新能源科技有限公司 | Solid electrolyte and preparation method thereof with include its electrochemical appliance and electronic device |
| CN109761265B (en) * | 2019-01-23 | 2020-08-14 | 宁德新能源科技有限公司 | Solid electrolyte, method of preparing the same, electrochemical device and electronic device including the same |
| US11588174B2 (en) | 2019-01-23 | 2023-02-21 | Ningde Amperex Technology Limited | Solid electrolyte and preparation method thereof, and electrochemical device and electronic device comprising solid electrolyte |
Also Published As
| Publication number | Publication date |
|---|---|
| CN100486024C (en) | 2009-05-06 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN100502111C (en) | Lithium-sulfur system solid electrolyte material for all solid state lithium battery and preparation method | |
| CN100524927C (en) | Solid electrolyte material system for all solid state lithium battery and preparation method | |
| Yao et al. | All-solid-state lithium batteries with inorganic solid electrolytes: Review of fundamental science | |
| Zhang et al. | Enhancing ionic conductivity of solid electrolyte by lithium substitution in halogenated Li-Argyrodite | |
| Duchardt et al. | Superion conductor Na11. 1Sn2. 1P0. 9Se12: lowering the activation barrier of Na+ conduction in quaternary 1–4–5–6 electrolytes | |
| Okumura et al. | LISICON-based amorphous oxide for bulk-type all-solid-state lithium-ion battery | |
| Tatsumisago et al. | Sulfide glass‐ceramic electrolytes for all‐solid‐state lithium and sodium batteries | |
| Knauth | Inorganic solid Li ion conductors: An overview | |
| Noi et al. | Structure and properties of the Na2S–P2S5 glasses and glass–ceramics prepared by mechanical milling | |
| Tatsumisago et al. | Superionic glasses and glass–ceramics in the Li2S–P2S5 system for all-solid-state lithium secondary batteries | |
| Kanno et al. | Synthesis of a new lithium ionic conductor, thio-LISICON–lithium germanium sulfide system | |
| Seino et al. | Synthesis of phosphorous sulfide solid electrolyte and all-solid-state lithium batteries with graphite electrode | |
| Minami et al. | Recent progress of glass and glass-ceramics as solid electrolytes for lithium secondary batteries | |
| CN108832172B (en) | All-solid-state electrolyte material, preparation method thereof and all-solid-state lithium secondary battery | |
| CN112018458B (en) | Sulfide-polymer composite solid electrolyte and preparation method and application thereof | |
| Li et al. | O‐Tailored microstructure‐engineered interface toward advanced room temperature all‐solid‐state Na batteries | |
| CN100486024C (en) | Lithium-lanthanum-silicon-sulfur solid electrolyte material for secondary lithium cell and its preparing method | |
| CN108390094A (en) | A kind of air-stable sulfide sodion solid electrolytes and preparation method thereof | |
| Lai et al. | Rapid sintering of ceramic solid electrolytes LiZr2 (PO4) 3 and Li1. 2Ca0. 1Zr1. 9 (PO4) 3 using a microwave sintering process at low temperatures | |
| CN108511795B (en) | O-shaped catalyst2-And F-Synergistically doped LISICON type solid electrolyte material and preparation method thereof | |
| Huan et al. | Factors influencing Li+ migration in garnet-type ceramic electrolytes | |
| CN100486025C (en) | Li2S-Al2S3 solid electrolyte material for secondary lithium cell and its preparing method | |
| Gao et al. | Sb‐and O‐Cosubstituted Li10SnP2S12 with High Electrochemical and Air Stability for All‐Solid‐State Lithium Batteries | |
| Roh et al. | Enhanced Li-Ion Conductivity and Air Stability of Sb-Substituted Li4GeS4 toward All-Solid-State Li-Ion Batteries | |
| Heo et al. | One‐pot aprotic solvent‐enabled synthesis of superionic Li‐argyrodite solid electrolyte |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| EE01 | Entry into force of recordation of patent licensing contract | ||
| EE01 | Entry into force of recordation of patent licensing contract |
Application publication date: 20070328 Assignee: FSPG Hi-Tech Co., Ltd. Assignor: Shanghai Silicates Institute, the Chinese Academy of Sciences Contract record no.: 2017310000043 Denomination of invention: Lithium-lanthanum-silicon-sulfur solid electrolyte material for secondary lithium cell and its preparing method Granted publication date: 20090506 License type: Common License Record date: 20170724 |