WO2020215921A1 - 一种全固态锂电池及其制备方法 - Google Patents

一种全固态锂电池及其制备方法 Download PDF

Info

Publication number
WO2020215921A1
WO2020215921A1 PCT/CN2020/079132 CN2020079132W WO2020215921A1 WO 2020215921 A1 WO2020215921 A1 WO 2020215921A1 CN 2020079132 W CN2020079132 W CN 2020079132W WO 2020215921 A1 WO2020215921 A1 WO 2020215921A1
Authority
WO
WIPO (PCT)
Prior art keywords
fast ion
ion conductor
borohydride
lithium
sulfide
Prior art date
Application number
PCT/CN2020/079132
Other languages
English (en)
French (fr)
Inventor
郑时有
庞越鹏
石鑫鑫
王曦童
王玉放
聂正方
Original Assignee
上海理工大学
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by 上海理工大学 filed Critical 上海理工大学
Priority to US16/964,206 priority Critical patent/US11349151B2/en
Priority to JP2020538989A priority patent/JP6979731B2/ja
Publication of WO2020215921A1 publication Critical patent/WO2020215921A1/zh

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
    • 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
    • H01M10/0525—Rocking-chair batteries, i.e. batteries with lithium insertion or intercalation in both electrodes; Lithium-ion batteries
    • 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
    • H01M10/058—Construction or manufacture
    • 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
    • H01M10/058—Construction or manufacture
    • H01M10/0585—Construction or manufacture of accumulators having only flat construction elements, i.e. flat positive electrodes, flat negative electrodes and flat separators
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/04—Processes of manufacture in general
    • H01M4/043—Processes of manufacture in general involving compressing or compaction
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/13—Electrodes for accumulators with non-aqueous electrolyte, e.g. for lithium-accumulators; Processes of manufacture thereof
    • H01M4/139—Processes of manufacture
    • H01M4/1391—Processes of manufacture of electrodes based on mixed oxides or hydroxides, or on mixtures of oxides or hydroxides, e.g. LiCoOx
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/13—Electrodes for accumulators with non-aqueous electrolyte, e.g. for lithium-accumulators; Processes of manufacture thereof
    • H01M4/139—Processes of manufacture
    • H01M4/1395—Processes of manufacture of electrodes based on metals, Si or alloys
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/36—Selection of substances as active materials, active masses, active liquids
    • H01M4/48—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides
    • H01M4/50—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides of manganese
    • H01M4/505—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides of manganese of mixed oxides or hydroxides containing manganese for inserting or intercalating light metals, e.g. LiMn2O4 or LiMn2OxFy
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/36—Selection of substances as active materials, active masses, active liquids
    • H01M4/48—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides
    • H01M4/52—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides of nickel, cobalt or iron
    • H01M4/525—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides of nickel, cobalt or iron of mixed oxides or hydroxides containing iron, cobalt or nickel for inserting or intercalating light metals, e.g. LiNiO2, LiCoO2 or LiCoOxFy
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/36—Selection of substances as active materials, active masses, active liquids
    • H01M4/58—Selection of substances as active materials, active masses, active liquids of inorganic compounds other than oxides or hydroxides, e.g. sulfides, selenides, tellurides, halogenides or LiCoFy; of polyanionic structures, e.g. phosphates, silicates or borates
    • H01M4/5825—Oxygenated metallic salts or polyanionic structures, e.g. borates, phosphates, silicates, olivines
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/62—Selection of inactive substances as ingredients for active masses, e.g. binders, fillers
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/62—Selection of inactive substances as ingredients for active masses, e.g. binders, fillers
    • H01M4/624—Electric conductive fillers
    • H01M4/625—Carbon or graphite
    • 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
    • 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 invention belongs to the field of new energy materials, and particularly relates to an all-solid-state lithium battery based on a borohydride/sulfide double-layer fast ion conductor and a preparation method thereof.
  • lithium metal is considered to be the most ideal negative electrode material for high-energy density batteries (its electrochemical potential is low, density is low, and theoretical capacity is high), lithium metal is very active and easily forms uncontrolled branches on the interface of lithium metal negative electrodes. Lithium may puncture the diaphragm during the cycle, causing internal short circuits and serious safety issues. Therefore, the use of inorganic solid electrolytes with high mechanical strength to prepare all-solid-state lithium batteries can not only solve the safety problems of organic liquid electrolytes, but also inhibit the growth of lithium dendrites, achieve high energy density, and provide the possibility for the development of new batteries.
  • solid electrolytes As a key component of all solid-state battery systems, solid electrolytes have received extensive attention from domestic and foreign researchers. According to its chemical composition, it can generally be divided into inorganic solid electrolyte, polymer solid electrolyte and composite solid electrolyte. Among them, the ionic conductivity of inorganic solid electrolytes represented by lithium lanthanum zirconium oxide and lithium germanium phosphorus sulfur has been greatly improved, and their ionic conductivity at room temperature can reach 10-3 ⁇ 10-2S cm-1[Adv .Mat.,2018,30(17):e1705702.], its value has approached or even exceeded the level of liquid electrolyte, which can basically meet the requirements of electrolyte conductivity in commercial batteries.
  • the inter-diffusion of the space charge layer and the elements can be inhibited to reduce the interface impedance [Chem.Mater.,2010,22(3):946-956.].
  • the interface layer usually contains components such as Li 2 S and Li 3 P.
  • the lithium ion conductivity is low, and the electronic conductivity is high.
  • the continuous interface reaction will also cause the interface to deteriorate and reduce the coulombic efficiency of the battery [Chem.Mater., 2016, 28(1):949-956.].
  • the all-solid-state battery assembled with sulfide as the electrolyte mainly uses Li-In alloy as the negative electrode, and its potential to Li/Li+ is about 0.6V, which reduces the working voltage of the battery and thus significantly reduces the energy density of the battery.
  • the positive electrode/garnet solid electrolyte interface also has problems such as element interdiffusion, volume expansion, and increase in interface impedance [J. Power Sources, 2014, 260:292-298.].
  • the garnet-type lithium lanthanum zirconium oxygen solid electrolyte has a low reduction potential for lithium (about 0.5V), the direct adhesion of metal lithium to the electrolyte has poor physical contact and very large interface impedance.
  • borohydride as a new type of solid electrolyte material, is stable to metal lithium due to its strong reducibility, and its grain boundary resistance is small and its mechanical deformation ability is strong.
  • Tohoku University Matsuo and others reported for the first time that lithium borohydride will change from the orthorhombic phase with low Li+ conductivity (10-8S cm-1,30°C) at room temperature to a hexagonal structure (10-3S cm-1,120) at around 110°C. °C). Subsequently, Maekawa et al.
  • lithium borohydride reacts with lithium cobalt oxide in a charged state to form LiBO 2, Li 2 O, Co 3 O 4, and CoO (OH), which causes an increase in interface impedance and causes battery failure.
  • the thickness of aluminum oxide must be ⁇ 1nm, because the ionic conductivity of these coating materials is very low. Lithium niobate can not achieve a good inhibitory effect. It will first react with lithium borohydride and be consumed, and then lithium borohydride will continue to react with lithium cobaltate [Solid State Ionics, 2014, 262: 179-182].
  • the technical problem to be solved by the present invention is that the solid electrolyte cannot be well compatible with the metal lithium negative electrode and the high-voltage positive electrode at the same time, which causes the lithium dendrite problem and the interface impedance problem of the all-solid-state battery, which seriously affects its large-scale commercial application.
  • the present invention provides an all-solid-state lithium battery based on a borohydride/sulfide double-layer fast ion conductor, which is characterized by comprising a borohydride fast ion conductor layer and a sulfide fast ion conductor layer.
  • the battery positive electrode is prepared by mixing a positive electrode active material, a sulfide fast ion conductor and a conductive agent in proportion; the battery negative electrode is a metal lithium sheet.
  • the borohydride fast ion conductor is any one of lithium borohydride, lithium borohydride-lithium iodide and closed lithium-boron-hydrogen composite fast ion conductor;
  • the sulfide fast ion conductor is lithium sulfide -Any one of phosphorus pentasulfide and lithium germanium phosphorus sulfur fast ion conductors.
  • the present invention also provides a method for preparing an all-solid-state lithium battery based on a borohydride/sulfide double-layer fast ion conductor, which is characterized in that it comprises the following steps:
  • Step 1 Cold press the borohydride fast ion conductor and the sulfide fast ion conductor into a double-layer electrolyte
  • Step 2 Mix the positive electrode active material, the sulfide fast ion conductor, and the conductive agent in proportion to serve as the positive electrode of the all-solid lithium battery, and cold press on the sulfide fast ion conductor side of the double-layer electrolyte obtained in step 1;
  • the sheet serves as the negative electrode of an all-solid-state lithium battery and is cold pressed on the side of the borohydride fast ion conductor of the double-layer electrolyte obtained in step 1;
  • Step 3 Encapsulate the material obtained in Step 2 to obtain an all-solid-state lithium battery based on a borohydride/sulfide double-layer fast ion conductor.
  • the borohydride fast ion conductor in the step 1 is any one of lithium borohydride, lithium borohydride-lithium iodide, and a closed lithium-boron-hydrogen composite fast ion conductor.
  • the sulfide fast ion conductor in step 1 and step 2 is any one of lithium sulfide-phosphorus pentasulfide and lithium germanium phosphorus sulfur fast ion conductor.
  • the pressure method of the cold pressing in the step 1 and step 2 is equiaxial pressure, the pressure is 100-500 MPa, and the pressure holding time is 5-20 min.
  • the shape of the double-layer electrolyte in the step 1 is a sheet with a total thickness of 0.1-5 mm, the thickness of the borohydride fast ion conductor layer is 10% to 90% of the total thickness, and the thickness of the sulfide fast ion conductor layer is the total thickness Of 10 to 90%.
  • the positive active material in the step 2 is any one of lithium iron phosphate, lithium cobalt oxide, lithium nickel manganese oxide, and lithium nickel cobalt manganese oxide.
  • the conductive agent in the step 2 is any one of carbon, copper and conductive polymer.
  • the packaging in step 3 is any one of button battery packaging, soft-pack battery packaging and solid-state battery mold packaging.
  • the present invention has the following beneficial effects:
  • the present invention fully combines the stability of the borohydride fast ion conductor to the metal lithium negative electrode and the stability of the sulfide fast ion conductor to the high voltage positive electrode, solves the problem of the compatibility of the positive and negative electrodes of the solid electrolyte, and obtains All solid-state batteries with high working voltage and good cycle performance.
  • Figure 1 is a schematic diagram of the structure of an all-solid-state lithium battery based on a borohydride/sulfide double-layer fast ion conductor; where 1 is a negative electrode, 2 is a borohydride fast ion conductor, 3 is a sulfide double-layer fast ion conductor, and 4 is positive electrode;
  • Figure 2 is a charge-discharge curve of an all-solid-state lithium battery with lithium cobalt oxide as the positive electrode, LiBH4-LiI/Li10GeP2S12 as the electrolyte and lithium metal as the negative electrode in Example 1;
  • Fig. 3 is a charge-discharge curve of an all-solid-state lithium battery in Example 2 with lithium iron phosphate as the positive electrode, LiBH4-LiI/70Li2S-30P2S5 as the electrolyte, and lithium metal as the negative electrode;
  • Fig. 4 shows the charge and discharge curve of an all-solid-state lithium battery in Example 3 with lithium nickel manganate as the positive electrode, Li2B12H12/Li3.25Ge0.25P0.75S4 as the electrolyte, and lithium metal as the negative electrode.
  • This embodiment provides a method for preparing an all-solid-state lithium battery based on a borohydride/sulfide double-layer fast ion conductor.
  • the specific preparation steps are as follows:
  • Step 1 Cold press 50mg LiBH4-LiI and 50mg Li10GeP2S 12 with 100MPa to form a double-layer electrolyte, hold the pressure for 5 minutes, the total thickness is 1.2mm, and the thickness of each layer is 0.6mm;
  • Step 2 Cold press 5mg of lithium cobalt oxide positive electrode (60wt% LiCoO 2, 30wt% Li 10 GeP 2 S 12, 10 wt% Ketjen Black through mixing and grinding) on the Li 10 GeP 2 S 12 of the double-layer electrolyte obtained in step 1 One side; use a metal lithium sheet (99.9%, Zhongneng Lithium) as the negative electrode of the all-solid lithium battery, and cold press it on the LiBH 4 -LiI side of the double-layer electrolyte obtained in step 1, the above cold pressure is 100Mpa, and the pressure is maintained 5min;
  • lithium cobalt oxide positive electrode 60wt% LiCoO 2, 30wt% Li 10 GeP 2 S 12, 10 wt% Ketjen Black through mixing and grinding
  • Step 3 Encapsulate the material obtained in Step 2 into a 2025 button battery to obtain an all-solid-state lithium battery based on a borohydride/sulfide double-layer fast ion conductor.
  • the prepared all-solid-state lithium battery was charged and discharged at a constant current of 0.05C at 55°C.
  • the test results are shown in Figure 2:
  • the constant current charge and discharge curve in Figure 2 shows the specific discharge capacity of the battery in the first cycle. It is 105 mAh g-1, after 100 cycles, the discharge specific capacity remains at 90 mAh g-1 (85.7% of the initial discharge specific capacity), the charging platform is as high as 3.9V, and the discharge platform is about 3.85V.
  • the above results show that the all-solid-state lithium battery with LiBH4-LiI/Li10GeP2S12 as the electrolyte can achieve long cycles and has a high capacity retention rate.
  • This embodiment provides a method for preparing an all-solid-state lithium battery based on a borohydride/sulfide double-layer fast ion conductor.
  • the specific preparation steps are as follows:
  • Step 1 Cold press 60mg LiBH 4 -LiI and 40mg 70Li 2 S-30P 2S 5 with 200MPa to form a double-layer electrolyte, hold the pressure for 20 minutes, the total thickness is 1.0mm, and the LiBH 4 -LiI layer thickness is 0.6mm, 70Li 2S -30P 2 S 5 layers with a thickness of 0.4mm;
  • Step 2 Cold press 5mg of lithium iron phosphate cathode (50wt% LiFePO 4,40wt% 70Li 2S-30P 2S 5,10wt% Ketjen Black through mixing and grinding) into the 70Li 2S- of the double-layer electrolyte obtained in step 1.
  • 30P 2 S 5 side use a metal lithium sheet (99.9%, Zhongneng Lithium) as the negative electrode of the all-solid lithium battery, and cold press it on the LiBH 4 -LiI side of the double-layer electrolyte obtained in step 1, above the cold pressure 200Mpa, keep pressure 20min;
  • Step 3 Encapsulate the material obtained in Step 2 into a 2032 button battery to obtain an all-solid lithium battery based on a borohydride/sulfide double-layer fast ion conductor.
  • the prepared all-solid-state lithium battery was charged and discharged at a constant current of 0.05C at 55°C.
  • the test results are shown in Figure 3:
  • the constant current charge and discharge curve in Figure 3 shows the specific discharge capacity of the battery in the first cycle. Up to 150mAh g-1, accounting for 88% of theoretical capacity.
  • the output voltage is around 3.2V, slightly lower than the 3.4V of the liquid electrolyte system.
  • the above results indicate that the borohydride/sulfide double-layer fast ion conductor electrolyte can also be applied to the lithium iron phosphate cathode, and its discharge specific capacity is similar to that of the liquid electrolyte system.
  • This embodiment provides a method for preparing an all-solid-state lithium battery based on a borohydride/sulfide double-layer fast ion conductor.
  • the specific preparation steps are as follows:
  • Step 1 Cold press 40mg Li 2 B 12 H 12 and 60 mg Li 3.25 Ge 0.25 P 0.75 S 4 into a double-layer electrolyte with 300 MPa cold pressing, and hold the pressure for 100 min.
  • the total thickness is 1.0 mm.
  • the thickness of the LiBH 4-LiI layer is 0.4 mm, 70 Li 2 S-30P 2 S 5 layers with a thickness of 0.6mm;
  • Step 2 Cold press 10mg of lithium nickel manganese oxide positive electrode (60wt% LiNi 0.5 Mn 1.5 O 4,40wt% 60Li 2 S-40P 2 S 5,10wt% Ketjen Black through mixing and grinding) into the double-layer electrolyte obtained in step 1.
  • the Li 3.25 Ge 0.25 P 0.75 S 4 side; the metal lithium sheet (99.9%, Zhongneng Lithium) is used as the negative electrode of the all-solid lithium battery, and it is cold pressed on the Li 2 B 12 H 12 of the double-layer electrolyte obtained in step 1.
  • the above cold pressure is 300Mpa, and the pressure is kept for 10min;
  • Step 3 Encapsulate the material obtained in Step 2 into a 2032 button battery to obtain an all-solid lithium battery based on a borohydride/sulfide double-layer fast ion conductor.
  • the prepared all-solid-state lithium battery was charged and discharged at a constant current of 0.05C at 75°C.
  • the test results are shown in Figure 4:
  • the constant current charge and discharge curve in Figure 4 shows that the structure is lithium nickel manganate
  • the first cycle discharge specific capacity of the Li battery is 69mAh g-1.
  • the test results show that the borohydride and sulfide double-layer fast ion conductor electrolyte can be used in voltage Up to about 4.7V lithium nickel manganese oxide positive electrode system.

Abstract

一种基于硼氢化物/硫化物双层快离子导体的全固态锂电池的制备方法，其特征在于，包括以下步骤：步骤1：将硼氢化物快离子导体（2）与硫化物快离子导体（3）冷压成双层电解质；步骤2：将正极活性物质、硫化物快离子导体和导电剂按比例混合，作为全固态锂电池的正极，并冷压于步骤1所得双层电解质的硫化物快离子导体（3）一侧；将金属锂片作为全固态锂电池的负极，并冷压于步骤1所得双层电解质的硼氢化物快离子导体（2）一侧；步骤3：将步骤2所得材料进行封装，得到基于硼氢化物/硫化物双层快离子导体的全固态锂电池。该全固态电池工作电压高、循环性能好，并且制备工艺简单，重复性好，适合大规模商业化生产。

Description

一种全固态锂电池及其制备方法 技术领域
本发明属于新能源材料领域，特别涉及基于硼氢化物/硫化物双层快离子导体的全固态锂电池及其制备方法。
背景技术
电池作为一种能量转换装置，在人们日常生活中应用极其广泛，但目前市售的电池(如铅酸电池，镍氢电池，锂离子电池，液流电池等)并不能满足人们在便携式电子设备、电动汽车以及大型储能系统方面日益增长的需求。过去大多数的电池研究都集中在有机液态电解质体系上，其化学稳定性和电化学稳定性差、离子选择性低，在过度充电、内部短路等异常时会引起电解液发热，有自燃甚至爆炸的危险。虽然锂金属被认为是制备高能量密度电池最理想的负极材料(其电化学势低、密度低、理论容量高)，但锂金属非常活泼，易在金属锂负极界面上形成不受控制的树枝状锂，在循环过程中可能会刺破隔膜，导致内部短路和严重的安全问题。所以采用机械强度高的无机固体电解质来制备全固态锂电池，不仅可以解决有机液态电解质的安全性问题，还可以抑制锂枝晶生长，实现高能量密度，为开发新型电池提供可能性。
固体电解质作为全固态电池体系中的关键组分，受到了国内外研究者的广泛关注。按照其化学组成通常可分为无机固体电解质、聚合物固体电解质和复合固体电解质。其中以锂镧锆氧和锂锗磷硫为代表的无机固体电解质的离子电导率得到了很大提升，它们在室温下的离子电导率可达10 -3～10 -2 S cm -1[Adv.Mat.,2018,30(17):e1705702.]，其数值已接近甚至超过液态电解质的水平，可基本满足商业电池中对电解质电导率的要求。然而在研发可实用化全固态电池的进程中，人们意识到固体电解质与正负极材料之间的界面问题会严重影响全固态电池的整体性能。硫化物固体电解质与电极材料的稳定性已经被大量研究，如在长循环过程中，正极/硫化物固体电解质界面处的阻抗会增大，造成电池容量衰减[ACS.Appl.Mater.Interfaces.,2018,10(26):22226-22236.]。如果在正极/硫化物固体电解质界面处进入缓冲层，则可以抑制空间电荷层和元素互扩散从而降低界面阻抗[Chem.Mater.,2010,22(3):946-956.]。理论计算和实验结果都表明,硫化物固体电解质对金属锂不稳定，与锂接触后会被锂还原形成界面层。界面层通常包含Li 2 S和Li 3 P等组分，其锂离子电导率低，电子电导率高，持续的界面反应还会导致界面劣化，降低电池的库伦效率[Chem.Mater.,2016,28(1):949-956.]。因此以硫化物为电解质组装的全固态电池主要使用Li-In合金作为负极，其对Li/Li+的电位约为0.6V，降低 了电池的工作电压,因而显著降低了电池的能量密度。同样，正极/石榴石型固体电解质界面也存在元素互扩散、体积膨胀、界面阻抗增大等问题[J.Power Sources,2014,260:292-298.]。虽然石榴石型锂镧鋯氧类固体电解质对锂的还原电位低(约为0.5V)，但直接将金属锂黏附在电解质上物理接触差，界面阻抗非常大。这类电解质的弹性形变较小，陶瓷片很容易破裂，而且晶界的大量存在会造成石榴石型固体陶瓷电解质并不能完全阻止锂枝晶的生长。故要实现全固态电池的高能量密度和长循环稳定性,固体电解质与正负极材料的界面问题至关重要。
在至今报道的各种固体电解质材料中，硼氢化物作为一类新的固体电解质材料，由于具有很强的还原性而对金属锂稳定，并且其晶界阻抗小，机械变形能力强。日本东北大学Matsuo等首次报道了硼氢化锂110℃左右会由室温下Li+导率低(10 -8 S cm -1,30℃)的斜方相转变为六方结构(10 -3 S cm -1,120℃)。随后Maekawa等发现通过添加锂的卤化物可以在室温下稳定硼氢化锂的高温相，并指出在超过40mA cm -2的高电流密度下，金属锂/硼氢化锂的界面仍可以保持稳定[J.Am.Chem.Soc.,2009,131:894.]。之后钛酸锂、二硫化钛、硫等活性物质被用于金属锂-硼氢化锂体系中，所组装的全固态电池具有高容量和优异的循环稳定性。但它们都属于低电压电极材料，即使是与金属锂匹配，所组装的电池电压也只有2V左右。Takahashi等发现硼氢化锂会与充电状态的钴酸锂发生反应生成LiBO 2、Li 2 O、Co 3 O 4和CoO(OH)，造成界面阻抗增大而使电池失效。他们采用脉冲激光沉积在钴酸锂表面包覆一层25nm厚的磷酸锂之后则可以有效抑制界面反应[J.Power Sources,2013,226:41-61.]。该课题组继续研究了用脉冲激光沉积分别在钴酸锂表面包覆不同厚度的磷酸锂、铌酸锂和三氧化二铝来抑制界面反应，结果表明磷酸锂的厚度须保持在10～25nm，三氧化二铝的厚度须<1nm，因为这些包覆层材料本身的离子电导率很低。而铌酸锂也不能达到很好的抑制效果，它会先与硼氢化锂反应而消耗掉，之后硼氢化锂会继续与钴酸锂反应[Solid StateIonics,2014,262:179-182]。
发明内容
本发明所要解决的技术问题是固体电解质无法同时很好兼容金属锂负极和高电压正极，导致全固态电池的锂枝晶问题和界面阻抗问题，严重影响了其大规模的商业化应用。
为解决上述技术问题，本发明提供了一种基于硼氢化物/硫化物双层快离子导体的全固态锂电池，其特征在于，包括硼氢化物快离子导体层与硫化物快离子导体层组成的双层电解质，电池正极，电池负极；所述电池正极位于硫化物快离子导体层一侧，电池负极位于硼氢化物快离子导体层一侧。
优选地，所述电池正极由正极活性物质、硫化物快离子导体和导电剂按比例混合制得；电池负极为金属锂片。
更优选的，所述硼氢化物快离子导体为硼氢化锂、硼氢化锂-碘化锂和闭式锂-硼-氢复合快离子导体中的任意一种；硫化物快离子导体为硫化锂-五硫化二磷类和锂锗磷硫类快离子导体中的任意一种。
本发明还提供了一种基于硼氢化物/硫化物双层快离子导体的全固态锂电池的制备方法，其特征在于，包括以下步骤：
步骤1：将硼氢化物快离子导体与硫化物快离子导体冷压成双层电解质；
步骤2：将正极活性物质、硫化物快离子导体和导电剂按比例混合，作为全固态锂电池的正极，并冷压于步骤1所得双层电解质的硫化物快离子导体一侧；将金属锂片作为全固态锂电池的负极，并冷压于步骤1所得双层电解质的硼氢化物快离子导体一侧；
步骤3：将步骤2所得材料进行封装，得到基于硼氢化物/硫化物双层快离子导体的全固态锂电池。
优选的，所述步骤1中硼氢化物快离子导体为硼氢化锂、硼氢化锂-碘化锂和闭式锂-硼-氢复合快离子导体中的任意一种。
优选的，所述步骤1和步骤2中硫化物快离子导体为硫化锂-五硫化二磷类和锂锗磷硫类快离子导体中的任意一种。
优选的，所述步骤1和步骤2中冷压成型的加压方式为等轴加压，压力大小为100～500MPa，保压时间为5～20min。
优选的，所述步骤1中双层电解质的形状为片状，总厚度0.1～5mm，硼氢化物快离子导体层厚度为总厚度的10～90％，硫化物快离子导体层厚度为总厚度的10～90％。
优选的，所述步骤2中正极活性物质为磷酸铁锂、钴酸锂、镍锰酸锂和镍钴锰酸锂中的任意一种。
优选的，所述步骤2中导电剂为碳、铜和导电高分子中的任意一种。
优选的，所述步骤3中封装为扣式电池封装、软包电池封装和固态电池模具封装中的任意一种。
与现有技术相比，本发明的有益效果在于：
(1)本发明充分结合了硼氢化物快离子导体对金属锂负极的稳定性和硫化物快离子导体对高电压正极的稳定性，解决了固体电解质的正负极相容性问题，得到了工作电压高、循环性能好的全固态电池。
(2)本发明所述制备工艺简单，重复性好，适合大规模商业化生产。
附图说明
图1为基于硼氢化物/硫化物双层快离子导体的全固态锂电池的结构示意图；其中1为负极，2为硼氢化物快离子导体，3为硫化物双层快离子导体，4为正极；
图2为实施例1中以钴酸锂为正极，LiBH4-LiI/Li10GeP2S12为电解质，金属锂为负极的全固态锂电池充放电曲线；
图3为实施例2中以磷酸铁锂为正极，LiBH4-LiI/70Li2S-30P2S5为电解质，金属锂为负极的全固态锂电池充放电曲线；
图4为实施例3中以镍锰酸锂为正极，Li2B12H12/Li3.25Ge0.25P0.75S4为电解质，金属锂为负极的全固态锂电池充放电曲线。
具体实施方式
下面结合具体实施例，进一步阐述本发明。应理解，这些实施例仅用于说明本发明而不用于限制本发明的范围。此外应理解，在阅读了本发明讲授的内容之后，本领域技术人员可以对本发明作各种改动或修改，这些等价形式同样落于本申请所附权利要求书所限定的范围。
实施例1
本实施例提供了一种基于硼氢化物/硫化物双层快离子导体的全固态锂电池的制备方法，具体制备步骤如下：
步骤1：将50mg LiBH 4 -LiI和50mg Li 10 GeP 2 S 12用100MPa冷压成双层电解质，保压5min，总厚度为1.2mm，每层厚度为0.6mm；
步骤2：将5mg钴酸锂正极(60wt％LiCoO 2,30wt％Li 10 GeP 2 S 12,10wt％科琴黑经混合研磨得到)冷压于步骤1所得双层电解质的Li 10 GeP 2 S 12一侧；将金属锂片(99.9％，中能锂业)作为全固态锂电池的负极，并冷压于步骤1所得双层电解质的LiBH 4 -LiI一侧，以上冷压压力100Mpa，保压5min；
步骤3：将步骤2所得材料封装成2025扣式电池，得到基于硼氢化物/硫化物双层快离子导体的全固态锂电池。
对所制备的全固态锂电池在55℃下，以0.05C进行恒电流充放电，测试结果如图2所示：从图2中的恒电流充放电曲线可以看出电池的首圈放电比容量为105mAh g-1，循环100圈之后放电比容量保持在90mAh g-1(为初始放电比容量的85.7％)，充电平台高达3.9V，放电平台为3.85V左右。以上结果表明以LiBH 4 -LiI/Li 10 GeP 2 S 12为电解质的全固态锂电池可以实现长循环，并且容量保持率高。
实施例2
本实施例提供了一种基于硼氢化物/硫化物双层快离子导体的全固态锂电池的制备方法，具体制备步骤如下：
步骤1：将60mg LiBH 4 -LiI和40mg 70Li 2 S-30P 2 S 5用200MPa冷压成双层电解质，保压20min，总厚度为1.0mm，LiBH 4 -LiI层厚度0.6mm，70Li 2 S-30P 2 S 5层厚度0.4mm；
步骤2：将5mg磷酸铁锂正极(50wt％LiFePO 4,40wt％70Li 2 S-30P 2 S 5,10wt％科琴黑经混合研磨得到)冷压于步骤1所得双层电解质的70Li 2 S-30P 2 S 5一侧；将金属锂片(99.9％，中能锂业)作为全固态锂电池的负极，并冷压于步骤1所得双层电解质的LiBH 4 -LiI一侧，以上冷压压力200Mpa，保压20min；
步骤3：将步骤2所得材料封装成2032扣式电池，得到基于硼氢化物/硫化物双层快离子导体的全固态锂电池。
对所制备的全固态锂电池在55℃下，以0.05C进行恒电流充放电，测试结果如图3所示：从图3中的恒电流充放电曲线可以看出电池的首圈放电比容量达150mAh g-1，占理论容量的88％。输出电压在3.2V左右，略低于液态电解质体系的3.4V。以上结果表明硼氢化物/硫化物双层快离子导体电解质也可适用于磷酸铁锂正极，并且其放电比容量与液态电解质体系相近。
实施例3
本实施例提供了一种基于硼氢化物/硫化物双层快离子导体的全固态锂电池的制备方法，具体制备步骤如下：
步骤1：将40mg Li 2 B 12 H 12和60mg Li 3.25 Ge 0.25 P 0.75 S 4用300MPa冷压成双层电解质，保压100min，总厚度为1.0mm，LiBH 4-LiI层厚度0.4mm，70Li 2 S-30P 2 S 5层厚度0.6mm；
步骤2：将10mg镍锰酸锂正极(60wt％LiNi 0.5 Mn 1.5 O 4,40wt％60Li 2 S-40P 2 S 5,10wt％科琴黑经混合研磨得到)冷压于步骤1所得双层电解质的Li 3.25 Ge 0.25 P 0.75 S 4一侧；将金属锂片(99.9％，中能锂业)作为全固态锂电池的负极，并冷压于步骤1所得双层电解质的Li 2 B 12 H 12一侧，以上冷压压力300Mpa，保压10min；
步骤3：将步骤2所得材料封装成2032扣式电池，得到基于硼氢化物/硫化物双层快离子导体的全固态锂电池。
对所制备的全固态锂电池在75℃下，以0.05C进行恒电流充放电，测试结果如图4所示：从图4中的恒电流充放电曲线可以看出结构为镍锰酸锂|Li 3.25 Ge 0.25 P 0.75 S 4/Li 2 B 12 H 12 |Li的电池首圈放电比容量为69mAh g-1，该测试结果 表明硼氢化物和硫化物双层快离子导体电解质可以应用在电压高达4.7V左右的镍锰酸锂正极体系。

Claims (1)

  1. 一种基于硼氢化物/硫化物双层快离子导体的全固态锂电池，其特征在于，包括硼氢化物快离子导体层与硫化物快离子导体层组成的双层电解质，电池正极，电池负极；所述电池正极位于硫化物快离子导体层一侧，电池负极位于硼氢化物快离子导体层一侧。2.如权利要求1所述基于硼氢化物/硫化物双层快离子导体的全固态锂电池，其特征在于，所述电池正极由正极活性物质、硫化物快离子导体和导电剂按比例混合制得；电池负极为金属锂片；所述硼氢化物快离子导体为硼氢化锂、硼氢化锂-碘化锂和闭式锂-硼-氢复合快离子导体中的任意一种；硫化物快离子导体为硫化锂-五硫化二磷类和锂锗磷硫类快离子导体中的任意一种。3.一种基于硼氢化物/硫化物双层快离子导体的全固态锂电池的制备方法，其特征在于，包括以下步骤：步骤1：将硼氢化物快离子导体与硫化物快离子导体冷压成双层电解质；步骤2：将正极活性物质、硫化物快离子导体和导电剂按比例混合，作为全固态锂电池的正极，并冷压于步骤1所得双层电解质的硫化物快离子导体一侧；将金属锂片作为全固态锂电池的负极，并冷压于步骤1所得双层电解质的硼氢化物快离子导体一侧；步骤3：将步骤2所得材料进行封装，得到基于硼氢化物/硫化物双层快离子导体的全固态锂电池。4.如权利要求3所述基于硼氢化物/硫化物双层快离子导体的全固态锂电池的制备方法，其特征在于，所述步骤1中硼氢化物快离子导体为硼氢化锂、硼氢化锂-碘化锂和闭式锂-硼-氢复合快离子导体中的任意一种。5.如权利要求3所述基于硼氢化物/硫化物双层快离子导体的全固态锂电池的制备方法，其特征在于，所述步骤1和步骤2中硫化物快离子导体为硫化锂-五硫化二磷类和锂锗磷硫类快离子导体中的任意一种。6.如权利要求3所述基于硼氢化物/硫化物双层快离子导体的全固态锂电池的制备方法，其特征在于，所述步骤1和步骤2中冷压成型的加压方式为等轴加压，压力大小为100～500MPa，保压时间为5～20min。7.如权利要求3所述基于硼氢化物/硫化物双层快离子导体的全固态锂电池的制备方法，其特征在于，所述步骤1中双层电解质的形状为片状，总厚度0.1～5mm，硼氢化物快离子导体层厚度为总厚度的10～90％，硫化物快离子导体层厚度为总厚度的10～90％。8.如权利要求3所述基于硼氢化物/硫化物双层快离子导体的全固态锂电池的制备方法，其特征在于，所述步骤2中正极活性物质为磷酸铁锂、钴酸锂、镍锰酸锂和镍钴锰酸锂中的任意一种。9.如权利要求3所述基于硼氢化物/硫化物双层快离子导体的全固态锂电池的制备方法，其特征在于，所述步骤2中导电剂为碳、铜和导电高分子中的任意一种。10.如权利要求3所述基于硼氢化物/硫化物双层快离子导体的全固态锂电池的制备方法，其特征在于，所述步骤3中封装为扣式电池封装、软包电池封装和固态电池模具封装中的任意一种。
PCT/CN2020/079132 2019-04-24 2020-03-13 一种全固态锂电池及其制备方法 WO2020215921A1 (zh)

Priority Applications (2)

Application Number Priority Date Filing Date Title
US16/964,206 US11349151B2 (en) 2019-04-24 2020-03-13 All-solid-state lithium battery and preparation method thereof
JP2020538989A JP6979731B2 (ja) 2019-04-24 2020-03-13 全固体リチウム電池及びその製造方法

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN201910332905.1 2019-04-24
CN201910332905.1A CN110061285A (zh) 2019-04-24 2019-04-24 一种全固态锂电池及其制备方法

Publications (1)

Publication Number Publication Date
WO2020215921A1 true WO2020215921A1 (zh) 2020-10-29

Family

ID=67320441

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2020/079132 WO2020215921A1 (zh) 2019-04-24 2020-03-13 一种全固态锂电池及其制备方法

Country Status (4)

Country Link
US (1) US11349151B2 (zh)
JP (1) JP6979731B2 (zh)
CN (1) CN110061285A (zh)
WO (1) WO2020215921A1 (zh)

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN110061285A (zh) * 2019-04-24 2019-07-26 上海理工大学 一种全固态锂电池及其制备方法
US11349150B2 (en) * 2019-08-01 2022-05-31 Toyota Motor Engineering & Manufacturing North America, Inc. Ceramic soft composites for solid-state batteries
CN111180789B (zh) * 2020-02-06 2021-08-27 华南理工大学 一种复合固态电解质材料及其制备方法和应用
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
CN114050311A (zh) * 2021-10-19 2022-02-15 复旦大学 一种联式硼笼离子化合物快离子导体材料及制备方法

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20180051717A (ko) * 2016-11-08 2018-05-17 한국에너지기술연구원 리튬 이온 전도성 복합 고체전해질, 그의 제조방법 및 그를 포함하는 리튬 전지
JP2018116784A (ja) * 2017-01-16 2018-07-26 株式会社日立製作所 固体電池用の正極材料、固体電池および固体電池の製造方法
CN207967198U (zh) * 2017-12-19 2018-10-12 成都亦道科技合伙企业（有限合伙） 一种锂金属负极电池结构
CN109411695A (zh) * 2018-10-31 2019-03-01 山东玉皇新能源科技有限公司 全固态锂离子电池正极极片及其制备方法
CN110061285A (zh) * 2019-04-24 2019-07-26 上海理工大学 一种全固态锂电池及其制备方法

Family Cites Families (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2011090794A (ja) * 2009-10-20 2011-05-06 Panasonic Corp 非水電解質二次電池用負極及び非水電解質二次電池
JP2013008586A (ja) * 2011-06-24 2013-01-10 Sony Corp リチウムイオン二次電池、リチウムイオン二次電池用負極、電池パック、電動車両、電力貯蔵システム、電動工具および電子機器
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
CA2922382C (en) * 2013-09-02 2022-04-05 Mitsubishi Gas Chemical Company, Inc. Solid-state battery in which lithium ions are responsible for electrical conduction
KR102355583B1 (ko) * 2014-12-22 2022-01-25 미츠비시 가스 가가쿠 가부시키가이샤 이온 전도체 및 그의 제조 방법
US9722279B2 (en) * 2014-12-24 2017-08-01 Toyota Motor Engineering & Manufacturing North America, Inc. All-solid-state metal-metal battery comprising ion conducting ceramic as electrolyte
JP2016134316A (ja) * 2015-01-20 2016-07-25 出光興産株式会社 固体電解質
JP6956641B2 (ja) * 2015-06-24 2021-11-02 クアンタムスケイプ バテリー， インク． 複合電解質
JP6183443B2 (ja) * 2015-12-10 2017-08-23 ソニー株式会社 リチウムイオン二次電池、リチウムイオン二次電池用負極、電池パック、電動車両、電力貯蔵システム、電動工具および電子機器
JP2019040709A (ja) * 2017-08-24 2019-03-14 株式会社日立製作所 全固体リチウムイオン二次電池およびその製造方法

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20180051717A (ko) * 2016-11-08 2018-05-17 한국에너지기술연구원 리튬 이온 전도성 복합 고체전해질, 그의 제조방법 및 그를 포함하는 리튬 전지
JP2018116784A (ja) * 2017-01-16 2018-07-26 株式会社日立製作所 固体電池用の正極材料、固体電池および固体電池の製造方法
CN207967198U (zh) * 2017-12-19 2018-10-12 成都亦道科技合伙企业（有限合伙） 一种锂金属负极电池结构
CN109411695A (zh) * 2018-10-31 2019-03-01 山东玉皇新能源科技有限公司 全固态锂离子电池正极极片及其制备方法
CN110061285A (zh) * 2019-04-24 2019-07-26 上海理工大学 一种全固态锂电池及其制备方法

Also Published As

Publication number Publication date
JP2021515353A (ja) 2021-06-17
US11349151B2 (en) 2022-05-31
US20210234192A1 (en) 2021-07-29
CN110061285A (zh) 2019-07-26
JP6979731B2 (ja) 2021-12-15

Similar Documents

Publication Publication Date Title
WO2020215921A1 (zh) 一种全固态锂电池及其制备方法
CN111554883B (zh) 一种基于干法制备电极膜的预锂化方法
CN101626099A (zh) 一种聚合物磷酸钒锂动力电池及其制备方法
CN101752562B (zh) 一种复合掺杂改性锂离子电池正极材料及其制备方法
CN101183730A (zh) 一种磷酸铁锂铝壳8安时圆柱电池及其制作工艺
CN114122409B (zh) 极片及锂离子电池
CN103247823B (zh) 全固态锂离子电池及其制备方法
CN103594735B (zh) 一种钛酸锂锂离子电池的制备方法
CN102479947A (zh) 一种锂离子电池正极材料及其制备方法、以及一种锂离子电池
CN101188310A (zh) 一种磷酸铁锂铝壳圆柱电池及其制作工艺
CN102157753A (zh) 快充高功率卷绕柱式锂离子电池
WO2022057189A1 (zh) 一种固态电池、电池模组、电池包及其相关的装置
CN102263287B (zh) 一种使用多相结构石墨为负极材料的锂离子电池
CN113078366A (zh) 一种软包装锂离子电池原位补锂及电池制造方法
CN101110477B (zh) 一种电化学储能与能量转换装置
CN101183731A (zh) 一种磷酸铁锂铝壳10安时圆柱电池及其制作工艺
CN116632320A (zh) 一种锂离子电池及包含其的用电装置
WO2024087368A1 (zh) 二次电池及用电装置
CN114122406B (zh) 石墨烯改性磷酸铁锂的制备方法及磷酸铁锂电池
CN102290603A (zh) 磷酸铁锂圆形电池及其制作工艺
WO2023077266A1 (zh) 二次电池及其补锂方法、电池模块、电池包及用电装置
CN101183732A (zh) 一种磷酸铁锂铝壳3.5安时圆柱电池及其制作工艺
CN212365998U (zh) 一种锂固态电池的电极构造
CN111224048B (zh) 富勒烯在固态电池中的应用和固态电池及其组装工艺
JP7389245B2 (ja) 二次電池及び該二次電池を備える装置

Legal Events

Date Code Title Description
ENP Entry into the national phase

Ref document number: 2020538989

Country of ref document: JP

Kind code of ref document: A

121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 20795347

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 20795347

Country of ref document: EP

Kind code of ref document: A1