Patent Application
20230231139
This application claims the priority benefit of China application serial no. 2021101172950, filed on Jan. 28, 2021, with the tile of invention “BINDER, NEGATIVE-ELECTRODE SLURRY, NEGATIVE ELECTRODE, AND LITHIUM-ION BATTERY”. The entirety of the above-mentioned patent application is hereby incorporated by reference herein.
Embodiments of the disclosure relate to a lithium-ion battery, and in particular to a binder, a negative-electrode slurry, a negative electrode, and a lithium-ion battery.
The negative-electrode binder is one of the important auxiliary functional materials in the lithium-ion battery and is the main source of internal mechanical properties of an electrode. The main function is to bond together an active material with an active material and a current collector with an active material. The traditional negative-electrode binders are mainly materials such as styrene-butadiene rubber, acrylic polymers, or acrylate polymers. Although these materials have strong binding force and good electrochemical stability, the materials are non-conductive, which may easily increase the internal impedance of the negative electrode, such that the fast charging performance of the lithium-ion battery deteriorates.
In order to solve the above issue, the following two methods are mainly adopted in the prior art. First, the affinity of the active material with the binder is improved. For example, Patent Publication No. JP 5373388 B2 discloses a method for mechanochemical processing of a graphite particle. The method enables the graphite particle to have a hydrophilic surface, a uniform particle diameter, a reduced average particle diameter, an improved surface wettability, and an increased affinity with a aqueous binder, which are beneficial to the improvement of the charging efficiency of the lithium-ion battery. However, the method requires the use of special graphite particle processing equipment that is costly and cannot achieve the same effect for a battery system in which the negative-electrode active material is not graphite (for example, silicon).
Second, the traditional binder is replaced with a binder with preferred ion-conducting capability. For example, Patent Publication No. CN 105489898 B discloses a conductive aqueous binder that can improve the overall conductivity of a battery and includes graphene, carbon nanotubes, a cross-linked polymer, and a polyvalent metal ion water-soluble salt solution, wherein the graphene and the carbon nanotubes are respectively bonded with the cross-linked polymer through chemical bonds to form a three-dimensional conductive network structure, and the cross-linked polymer is cross-linked with the polyvalent metal ion water-soluble salt solution to form a three-dimensional binding network structure. However, since the conductive aqueous binder is mainly a combination of various existing materials, the components is complex, the cost of raw materials used for preparing the conductive aqueous binder is high, it is difficult to promote on a large scale, and there is an incompatibility issue when the conductive aqueous binder is applied to the negative electrode of a silicon system.
Patent Publication No. CN 108417836 A discloses a binder for an electrode of an ABA type triblock polymer. The two ends are polyacrylic blocks and the center is a polyacrylate block. The polyacrylic block is polymerized from a methacrylic monomer and/or an acrylic monomer, and the polyacrylate block is polymerized from one or more of methyl acrylate, butyl acrylate, hydroxyethyl acrylate, and hydroxypropyl acrylate. Since the polyacrylate block has a certain swelling capability on an electrolyte to form an ion-conducting channel, the ion-conducting capability of the binder can be improved to a certain extent. However, the inventors found that since the modulus of the binder for the electrode of the ABA type triblock polymer is too high, and the use of the binder alone causes the rigidity of an electrode piece to be too strong, causing an electrode material to fall off a foil.
Therefore, it is still required in the art to find a negative-electrode binder having strong ion-conducting capability, simple components, low cost, suitable modulus, and good thickening and dispersing effects, while being compatible with various negative-electrode systems and easy to promote on a large scale.
The objective of the embodiments of the disclosure is to provide a binder having strong ion-conducting capability, simple components, low cost, suitable modulus, and good thickening and dispersing effects, so that a lithium-ion battery using the binder has preferred fast charging capability, low direct current internal resistance, and preferred low temperature discharge capability.
In order to solve the above technical issue, an embodiment of the disclosure provides a binder, and the binder includes a first block polymer and a second block polymer; the first block polymer is a lithiated tetrablock polymer, and the tetrablock polymer has a structure shown as B-C-B-A, wherein A represents a polymer block A, B represents a polymer block B, and C represents a polymer block C;
the polymer block A is polymerized from an alkenyl formic acid monomer;
the polymer block B is polymerized from an aromatic vinyl monomer;
the polymer block C is polymerized from an acrylate monomer; and
the second block polymer is a lithiated triblock polymer, and the triblock polymer has a structure shown as E-F-E, wherein E represents a polymer block E, and F represents a polymer block F;
the polymer block E is polymerized from an alkenyl formic acid monomer;
the polymer block F is polymerized from an acrylate monomer.
In some preferred solutions, a structure of the alkenyl formic acid monomer in the tetrablock polymer is
wherein R11 and R12 are independently hydrogen or a C1-4 alkyl group, and the C1-4 alkyl group is selected from a methyl group, an ethyl group, an n-propyl group, an isopropyl group, an n-butyl group, an isobutyl group, or a tert-butyl group; preferably, the alkenyl formic acid is an acrylic acid.
In some preferred solutions, a structure of the aromatic vinyl monomer in the tetrablock polymer is
are R21, R22, R23, R24, R25, and R26 are independently hydrogen or a C1-4 alkyl group, and the C1-4 alkyl group is selected from a methyl group, an ethyl group, an n-propyl group, an isopropyl group, an n-butyl group, an isobutyl group, or a tert-butyl group; preferably, R21, R22, R23, R24, R25, and R26 are hydrogen or the methyl group, more preferably, the aromatic vinyl is styrene.
In some preferred solutions, a structure of the acrylate monomer in the tetrablock polymer is
wherein R31 is a linear or branched C1-10 alkyl group; more preferably, R31 is a linear or branched C4-8 alkyl group, further preferably, R31 is
In some preferred solutions, the first block polymer has a structure shown as Formula (I):
wherein n is 10˜50; x is 200˜500; y is 400˜1000; z is 200˜500;
R41 is a C4-8 alkyl group; preferably, R41 is
R42 and R43 are a phenyl group or a C1-4 alkyl group substituted phenyl group, and the phenyl group of the C1-4 alkyl group is selected from a methyl group, an ethyl group, an n-propyl group, an isopropyl group, an n-butyl group, an isobutyl group, or a tert-butyl group substituted phenyl groups; preferably, R42 and R43 are the phenyl groups.
In some preferred solutions, the first block polymer is
wherein n is 10˜50; x is 200˜500; y is 400˜1000; z is 200˜500.
In some preferred solutions, the alkenyl formic acid in the triblock polymer is
wherein R51 and R52 are independently hydrogen or a C1-4 alkyl group, and the C1-4 alkyl group is selected from a methyl group, an ethyl group, an n-propyl group, an isopropyl group, an n-butyl group, an isobutyl group, or a tert-butyl group; preferably, the alkenyl formic acid is an acrylic acid.
In some preferred solutions, the acrylate in the triblock polymer is
wherein R61 is a C1-4 alkyl group, the C1-4 alkyl group is selected from a methyl group, an ethyl group, an n-propyl group, an isopropyl group, an n-butyl group, an isobutyl group, or a tert-butyl group; preferably, the acrylate is methyl acrylate.
In some preferred solutions, a degree of polymerization of the polymer block E is 70˜700, and a degree of polymerization of the polymer block F is 70˜700.
In some preferred solutions, the second block polymer has a structure shown as Formula (II);
wherein k is 70˜700; 1 is 70˜700; m is 70˜700.
In some preferred solutions, a mass ratio of the first block polymer to the second block polymer is 99:1˜1:99; more preferably, 9:1˜1:9, such as 9:1, 8:2, 7:3, 6:4, 5:5, 4:6, 7:3, 8:2, or 1:9.
In some more preferred solutions, the mass ratio of the first block polymer to the second block polymer is 9:1.
A second aspect of the disclosure provides a negative-electrode slurry for a lithium-ion battery, and the negative-electrode slurry includes a negative-electrode active material, a conductive agent, and the binder described in the first aspect of the disclosure.
In some preferred solutions, a mass ratio of the negative-electrode active material to the conductive agent to the binder is a:b:c, wherein a is 93˜97; b is 3-5; c is 3-5, and a+b+c=100. For example, 95:2:3.
A third aspect of the disclosure also provides a negative electrode of a lithium-ion battery including the negative-electrode slurry, the negative electrode includes a current collector and a negative-electrode active material layer coated on the current collector, and the negative-electrode active material layer is formed by coating the negative-electrode slurry on the current collector.
The negative-electrode active material of the negative electrode of the disclosure is a material that can be intercalated in and deintercalated from lithium, which includes, but is not limited to, a carbon material such as crystalline carbon (natural graphite, artificial graphite, etc.), amorphous carbon, carbon-coated graphite, and resin-coated graphite, and an oxide material such as indium oxide, silicon oxide, tin oxide, lithium titanate, zinc oxide, and lithium oxide. The negative-electrode active material may also be lithium metal or a metal material that can form an alloy with lithium. Specific examples of the metal that can form an alloy with lithium include Cu, Sn, Si, Co, Mn, Fe, Sb, and Ag. A binary or ternary alloy containing the metals and lithium may also be used as the negative-electrode active material. The negative-electrode active materials may be used alone or in combination of two or more. From the viewpoint of high energy density, as the negative-electrode active material, a carbon material such as graphite and a Si-based active material such as Si, a Si alloy, and a silicon oxide may be combined. From the viewpoint of achieving both cycle characteristic and high energy density, as the negative-electrode active material, graphite and a Si-based active material may be combined. Regarding the combination, the ratio of the mass of the Si-based active material to the total mass of the carbon material and the Si-based active material may be 0.5% or more and 95% or less, 1% or more and 50% or less, or 2% or more and 40% or less. In various embodiments, the negative-electrode active material is dispersed in the dense cross-linked network structure.
Preferably, the negative-electrode active material includes graphite and/or a graphite-containing compound.
The conductive agent of the negative electrode of the disclosure is a conductive material that does not cause chemical changes and may be at least one selected from natural graphite, artificial graphite, carbon black, acetylene black, carbon fiber, a polyphenylene derivative, metal powders including copper, nickel, aluminum, and silver, and metal fiber.
The current collector of the negative electrode of the disclosure may be at least one selected from a copper foil, a nickel foil, a stainless steel foil, a titanium foil, a nickel foam, a copper foam, and a conductive metal-coated polymer material.
A fourth aspect of the disclosure provides a lithium-ion battery, and the lithium-ion battery includes a positive electrode, a negative electrode, a separator, and an electrolyte, wherein the negative electrode is the negative electrode provided by the fourth aspect of the disclosure.
The positive electrode of the lithium-ion battery of the disclosure includes a positive-electrode active material, and the positive-electrode active material may be a lithium-containing composite oxide. Specific examples of the lithium-containing composite oxide include, for example, LiMnO2, LiFeO2, LiMn2O4, Li2FeSiO4, LiNi1/3 Co1/3Mn1/3O2, LiNi5CO2Mn3O2, LizNi(1-x-y)CoxMyO2 (x, y, and z are values satisfying 0.01≤x≤0.20, 0≤y≤0.20, and 0.97≤z≤1.20, and M represents at least one element selected from Mn, V, Mg, Mo, Nb, and Al), LiFePO4, and LizCO(1-x)MxO2 (x and z are values satisfying 0≤x≤0.1 and 0.97≤z≤1.20, and M represents at least one element selected from a group composed of Mn, Ni, V, Mg, Mo, Nb, and Al). The positive-electrode active material may also be LizNi(1-x-y)CoxMyO2 (x, y, and z are values satisfying 0.01≤x≤0.15, 0≤y≤0.15, and 0.97≤z≤1.20, and M represents at least one element selected from Mn, Ni, V, Mg, Mo, Nb, and Al) or LizCO(1-x)MxO2 (x and z are values satisfying 0≤x≤0.1 and 0.97≤z≤1.20, and M represents at least one element selected from Mn, V, Mg, Mo, Nb, and Al).
Preferably, the positive-electrode active material is NCM523.
The separator of the lithium-ion battery of the disclosure is not particularly limited and a single-layer or laminated microporous film, woven fabric, non-woven fabric, etc. of polyolefin such as polypropylene and polyethylene may be used.
The non-aqueous electrolyte of the lithium-ion battery of the disclosure is not particularly limited and an electrolyte formulation commonly used in the art may be used, which will not be described in detail here.
On the basis of not violating common knowledge in the art, the above preferred conditions may be combined arbitrarily to obtain preferred examples of the disclosure.
Reagents and raw materials used in the disclosure are all commercially available.
Compared with the prior art, the embodiments of the disclosure have at least the following advantages:
(1) The binder provided by the first aspect of the disclosure has preferred ion-conducting capability, which helps to reduce the internal resistance of the electrode.
(2) The binder provided by the first aspect of the disclosure has preferred binding force while having preferred dispersing and thickening effects, and has a suitable modulus.
(3) Using the lithiated block polymer of the disclosure as the binder, the prepared lithium-ion battery has preferred fast charging capability, lower direct current internal resistance, and preferred low temperature discharge capability.
In order for the objectives, technical solutions, and advantages of the embodiments of the disclosure to be clearer, each embodiment of the disclosure will be described in detail below with reference to specific examples. However, it should be understood that persons skilled in the art will appreciate that in each embodiment of the disclosure, numerous technical details are set forth in order to provide the reader with a better understanding of the present application. However, even without the technical details and various changes and modifications based on the following embodiments, the technical solutions claimed in the present application may still be implemented. In the following examples, experimental methods without specific conditions are usually in accordance with conventional conditions or in accordance with conditions suggested by the manufacturer. Percentages and parts are calculated by weight unless otherwise indicated.
1.0 g of 2-mercapto-S-thiobenzoylacetic acid (molecular weight of 212.3 g/mol) was weighed, mixed with 3.0˜17.0 g of refined acrylic monomer, and poured into a 500 mL three-necked flask. Another 0.2˜0.5 g of potassium persulfate was weighed, dissolved in 5˜10 g of deionized water and stored at low temperature for later use. The flask was placed on a water bath cauldron, added with magnets, stirred and dissolved at room temperature, then passed nitrogen for 30 min to remove oxygen therein, heated to 60˜80° C., added with the potassium persulfate aqueous solution, reacted for 12˜20 hours, and the polyacrylic acid (PAA) was obtained.
98.0˜245.0 g of styrene monomer was weighed, slowly added into the flask after the reaction in Step 1 through a syringe, continued reacting at 60˜80° C. for 2˜8 hours, and the polyacrylic acid-styrene (PAA-PSt) was obtained.
347.0˜866.0 g of isooctyl acrylate monomer was weighed, slowly added into the flask after the reaction in Step 2 through a syringe, continued reacting at 60˜80° C. for 2˜6 h, and the polyacrylic acid-styrene-isooctyl acrylate (PAA-PSt-PEHA) was obtained.
98.0˜245.0 g of styrene monomer was weighed, slowly add into the flask after the reaction in Step 3 through a syringe, continued reacting at 60˜80° C. for 2˜8 hours, the reacted product was washed with deionized water until the pH is 3˜6, and the polyacrylic acid-styrene-isooctyl acrylate-styrene (PAA-PSt-PEHA-PSt) was obtained.
500 g of the polyacrylic acid-styrene-isooctyl acrylate-styrene (PAA-PSt-PEHA-PSt) obtained in Step 4 and 15˜25 g of lithium hydroxide solution with a mass fraction of 5%˜15% (containing 0.75˜3.75 g of lithium hydroxide) were taken, stirred at a rotational speed of 300 rpm/h for 60 minutes, and the lithiated polyacrylic acid-styrene-isooctyl acrylate-styrene (PAA-PSt-PEHA-PSt) was obtained.
0.6 parts of RAFT reagent, 0.2 parts of initiator, and 20 parts of acrylic monomer were in 150 parts of deionized water solvent, stirred at 70° C. for 18 hours, and a reaction mixture containing the compound of Formula (1′) was obtained; wherein the RAFT reagent was
wherein R was an acetate group; Z was a benzyl group; the initiator was potassium persulfate.
60 parts of methyl acrylate monomer was added into the reaction mixture obtained in Step 1, then continued stirring 70° C. for 6 hours, and a reaction mixture containing the compound of Formula (2′) was obtained.
20 parts of acrylic acid monomer was added into the reaction mixture obtained in Step 2, then continued stirring at 70° C. for 18 hours, and a reaction mixture containing the compound of Formula (3′) was obtained.
The pH of the reaction mixture obtained in Step 3 was adjusted to 5, a lithium hydroxide aqueous solution with a mass fraction of 10% was added, and lithiated at 25° C. for 4 hours.
After the lithiation reaction was completed, the reaction mixture was precipitated, washed, and dried, and the lithiated polyacrylic acid-methyl acrylate-acrylic acid (PAALi-PMA-PAALi) shown as Formula (I′) was obtained. The molecular weight of the finally obtained polymer was about 20,000.
The lithiated polyacrylic acid-styrene-isooctyl acrylate-styrene (PAALi-PSt-PEHA-PSt) prepared in Example 1 and the lithiated polyacrylic acid-methyl acrylate-acrylic acid (PAALi-PMA-PAALi) prepared in Example 2 were stirred and mixed according to the mass ratio of 9:1, the stirring speed was 200 rpm, the temperature was 30° C., and the time was 2 hours.
Preparation of a Positive Electrode Piece
A positive-electrode active material NCM523, conductive carbon black Super-P, and binder polyvinylidene fluoride (PVDF) were mixed in a mass ratio of 96:2:2, then dispersed in N-methyl-2-pyrrolidone (NMP), and a positive-electrode slurry was obtained. The obtained positive-electrode slurry was evenly coated on two surfaces of an aluminum foil, dried, calendered, and vacuum-dried at 80°, an aluminum lead wire was welded using an ultrasonic welder, a positive electrode plate was obtained, and the thickness of the plate was 120˜150 μm.
Preparation of a Negative Electrode Piece
Composite negative-electrode active material graphite, conductive carbon black Super-P, and the binder prepared in Example 3 were mixed in a mass ratio of 95:2:3, then dispersed in deionized water, and a negative-electrode slurry was obtained. The slurry was coated on two surfaces of a copper foil, dried, calendered, and vacuum-dried, a nickel lead wire was welded using an ultrasonic welder, a negative electrode plate was obtained, and the thickness of the plate was 80˜100 μm.
Preparation of a Core
A separator with a thickness of 20 μm was placed between the positive electrode plate and the negative electrode plate, a sandwich structure composed of the positive electrode plate, the negative electrode plate, and the separator was then wound, the wound body was flattened and placed in an aluminum foil packaging bag, vacuum-baked at 85° C. for 48 h, and the core to be injected was obtained.
Core Injection
An electrolyte was injected into the core in a glove box, vacuum-sealed, and kept at rest for 24 h. Then, the routinization of the first charging was performed according to the following steps of: charging to 3.05 V with 0.02 C constant current, charging to 3.75 V with 0.05 C constant current, charging to 4.05 V with 0.2 C constant current, and vacuum-sealed. Then, further charged to 4.2 V with 0.33 C constant current, and after being left at room temperature for 24 hours, discharged to 3.0 V with 0.2 C constant current.
For Example 13 to Example 20, the lithium-ion battery was prepared according to the same method as Example 12, and the difference was that in the preparation of the negative electrode piece, the binder used was respectively the binder prepared in Example 3 to Example 11.
Preparation of a Positive Electrode Piece
A positive-electrode active material NCM523, conductive carbon black Super-P, and binder polyvinylidene fluoride (PVDF) were mixed in a mass ratio of 96:2:2, then dispersed in N-methyl-2-pyrrolidone (NMP), and a positive-electrode slurry was obtained. The obtained positive-electrode slurry was evenly coated on two surfaces of an aluminum foil, dried, calendered, and vacuum-dried at 80°, an aluminum lead wire was welded using an ultrasonic welder, a positive electrode plate was obtained, and the thickness of the plate was 120˜150 μm.
Preparation of a Negative Electrode Piece
Composite negative-electrode active material graphite, conductive carbon black Super-P, and PAA binder were mixed in a mass ratio of 95:2:3, then dispersed in deionized water, and a negative-electrode slurry was obtained. The slurry was coated on two surfaces of a copper foil, dried, calendered, and vacuum-dried, a nickel lead wire was welded using an ultrasonic welder, a negative electrode plate was obtained, and the thickness of the plate was 80˜100 μm.
Preparation of a Core
A separator with a thickness of 20 μm was placed between the positive electrode plate and the negative electrode plate, a sandwich structure composed of the positive electrode plate, the negative electrode plate, and the separator was then wound, the wound body was flattened and placed in an aluminum foil packaging bag, vacuum-baked at 85° C. for 48 h, and the core to be injected was obtained.
Core Injection
An electrolyte was injected into the core in a glove box, vacuum-sealed, and kept at rest for 24 h. Then, the routinization of the first charging was performed according to the following steps of: charging to 3.05 V with 0.02 C constant current, charging to 3.75 V with 0.05 C constant current, charging to 4.05 V with 0.2 C constant current, and vacuum-sealed. Then, further charged to 4.2 V with 0.33 C constant current, and after being left at room temperature for 24 hours, discharged to 3.0 V with 0.2 C constant current.
For Comparative Example 2, the lithium-ion battery was prepared according to the same method as Comparative Example 1, and the difference was that in the preparation of the negative electrode piece, the binder used was an SBR binder.
For Comparative Example 3, the lithium-ion battery was prepared according to the same method as Comparative Example 1, and the difference was that in the preparation of the negative electrode piece, the binder used was only lithiated polyacrylic acid-styrene-isooctyl acrylate-styrene (PAALi-PSt-PEHA-PSt).
For Comparative Example 4, the lithium-ion battery was prepared according to the same method as Comparative Example 1, and the difference was that in the preparation of the negative electrode piece, the binder used was only lithiated polyacrylic acid-methyl acrylate-acrylic acid (PAALi-PMA-PAALi).
(1) Tensile Performance Test of the Binder
The binder prepared in Example 3 was made into a film, and the preparation process was as follows: 1.2 g of the binder was poured into a polytetrafluoroethylene watch glass with a diameter of 10 cm, covered with a layer of filter paper, the filter paper was held down, placed into a fume hood, dried in convection at room temperature for a week, then placed into a vacuum oven at 60° C., vacuum-dried for 12 h, and sample preparation was completed.
Dumbbell-shaped splines were cut on a cutting machine according to the dimensions indicated for Type 2 and Type 4 specimens in ISO 37-1994 and implemented in accordance with the GB 16421-1996 standard, and the number of splines for each polymer was 5. The tensile test was performed using a universal material testing machine. Test conditions: a force sensor with a range of 50 N was used, the tensile rate was 1 mm/min, each polymer sample was subjected to 5 parallel tests, and an average value was obtained. The results obtained are shown in Table 2.
The tensile performance test of the binder, the PAA binder, the SBR binder, the lithiated polyacrylic acid-styrene-isooctyl acrylate-styrene (PAALi-PSt-PEHA-PSt), and the lithiated polyacrylic acid-methyl acrylate-acrylic acid (PAALi-PMA-PAALi) prepared in Examples 4 to 11 were according to the same method. The results obtained are shown in Table 2.
(2) Fast Charging Capability Test
At 25° C., a constant current charging test was performed on the lithium-ion battery prepared in the examples and the comparative examples by adopting a rate of 2 C, a rate charging capacity retention rate was calculated (the charging retention rate of a battery at the rate of 2 C=the capacity released after the battery is charged at the rate of 2 C/the capacity released after the battery is charged at a rate of 1/3 C). The results obtained are shown in Table 3.
(3) Direct Current Internal Resistance (DCR) Test
At 25° C., the battery prepared in the examples and the comparative examples was respectively discharged at 4 C for 30 s at a state of charge (SOC) of 50%, and the direct current internal resistance R=−(V1−V2)/I, wherein V1 is the voltage before discharge, V2 is the voltage after discharge, and I is the discharge current, and the direct current internal resistance was calculated. The results obtained are shown in Table 3.
(4) Low Temperature Discharge Capability Test
The battery prepared in the examples and the comparative examples was taken, and a discharge capacity retention rate at −20° C. was measured: at 25° C., the fully charged battery was discharged to 3.0 V at 1 C, and an initial discharge capacity was recorded as DC (25° C.). Then, at 25° C., charged to 4.2 V with 1 C constant current and constant voltage, and the cut-off current was 0.05 C. Then, cooled to −20° C., kept at rest for 4 h, then discharged to 3.0 V at 1 C, and the discharge capacity DC (−20° C.) was recorded. At −20° C., the discharge capacity retention rate=100%*DC (−20° C.)/DC (25° C.). The results obtained are shown in Table 3.
Persons skilled in the art can understand that the above examples are specific examples for implementing the disclosure. However, in practical applications, various changes in form and details may be made without departing from the spirit and the scope of the disclosure.
| Number | Date | Country | Kind |
|---|---|---|---|
| 202110117295.0 | Jan 2021 | CN | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/CN2021/076032 | 2/8/2021 | WO |
