Patent Application
20190181427
The present invention relates to an anode composition for lithium ion batteries, a process for preparing an anode for lithium ion batteries, and a lithium ion battery.
Lithium ion batteries have now been widely used in energy storage systems and electric vehicles.
Silicon is a promising active material for electrodes of lithium ion batteries owning to its large theoretical capacity and moderate operating voltage. However, during the lithiation/delithiation processes, silicon undergoes dramatic expansion and contraction. Such huge volumetric change impairs the electrochemical performances of lithium ion batteries.
There is an on-going demand for more attractive and reliable lithium ion batteries.
On the other hand, in the effort to design a high-power battery, the reduction of active material particle size to nano-scale can help shorten the diffusion length of charge carriers, enhance the Li-ion diffusion coefficient, and therefore achieve faster reaction kinetics. However, nano-sized active materials have a large surface area, which results in a high irreversible capacity loss due to the formation of a solid electrode interface (SEI). For silicon oxide based anode, the irreversible reaction during the first lithiation also leads to a large irreversible capacity loss in initial cycle. This irreversible capacity loss consumes Li in the cathode, which decreases the capacity of the full cell.
Even worse, for Si-based anode, repeated volume change during cycling reveals more and more fresh surface on the anode, which leads to continuous growth of SEI. And the continuous growth of SEI continuously consumes Li in the cathode, which results in capacity decay for the full cell.
In order to provide more lithium ions to compensate for an SEI or other lithium consumption during the formation, additional or supplementary Li may be provided by the prelithiation of the anode. If the prelithiation of the anode is conducted, the irreversible capacity loss could be compensated in advance instead of Li consumption from the cathode. This results in higher efficiency and capacity of the cell.
However, a pre-lithiation degree of exact compensation for the irreversible loss of lithium from the anode doesn't help to solve the problem of Li consumption from the cathode during cycling. Therefore, in this case, the cycling performance will not be improved. To compensate for the loss of lithium from the cathode during cycling, an over-prelithiation is conducted in the present invention.
After intensive study, the inventors have now developed a novel anode composition for lithium ion batteries, comprising:
Y—(CH2)n—Si—X3 (1)
Optionally, the anode composition according to the present disclosure may further comprise: d) a carbon material, wherein the carbon material may be selected from the group consisting of carbon black, super P, acetylene black, Ketjen black, graphite, graphene, carbon nanotubes and vapour grown carbon fibers.
Optionally, the anode composition according to the present disclosure may further comprise: e) a chain extender, which copolymerizes with the conductive polymer moiety obtainable from the silane coupling agent. Preferably, the chain extender may be selected from the group consisting of aniline, pyrrole, thiophene and their derivatives.
In some examples, the anode composition according to the present disclosure may comprise:
Also provided is a process for preparing an anode, comprising:
Also provided is a lithium ion battery, comprising an anode prepared from the anode composition according to the present disclosure, or an anode prepared by the process according to the present disclosure.
Surprisingly, the inventors found that by employing the anode composition according to the present invention, the lithium ion battery exhibits excellent electrochemical properties, including cycling performance and rate performance.
These and other features, aspects and advantages of the present disclosure will become evident to those skilled in the art from the following description of various examples taken in conjunction with the accompanying drawings.
Reference will now be made to some illustrative examples, and specific language will be used herein to describe the same. It will nevertheless be understood that no limitation of the scope of the disclosure is thereby intended.
Throughout this disclosure, all the scientific and technical terms, unless otherwise indicated, shall have the same meanings as those known to a person skilled in the art. Where there is inconsistency, the definition provided in the present disclosure should be taken.
It should be understood that the detailed description of all materials, processes, examples and drawings are presented for the purposes of illustration, and therefore, unless expressly specified otherwise, are not construed as limitations of the present disclosure.
Herein, the terms “cell” and “battery” may be interchangeably used. The terms “lithium ion cell” or “lithium ion battery” may also be abbreviated to “cell” or “battery”.
Herein, the term “comprising” means that other ingredients or other steps which do not affect the final effect can be included. This term encompasses the terms “consisting of” and “consisting essentially of”. The product and process according to the present disclosure can comprise, consist of, and consist essentially of the essential technical features and/or limitations of the present disclosure described herein, as well as any additional and/or optional ingredients, components, steps, or limitations described herein.
The use of the terms “a”, “an” and “the” and similar referents in the context of describing the subject matter of this application (especially in the context of the following claims) are to be construed to cover both the singular and the plural, unless otherwise indicated herein or clearly contradicted by context.
Unless otherwise specified, every numerical range in this context intends to include both endpoints and any numbers and sub-ranges falling within said numerical ranges.
Unless specially indicated, all materials and agents used in the present disclosure are commercially available.
Examples of the present disclosure are described in detail as follows.
According to some examples of the present disclosure, the anode composition for lithium ion batteries may comprise a silicon-based active material. Comparing with a carbon-based active material, a silicon-based active material possesses a larger theoretical capacity and a more moderate operating voltage.
The term “active material” as used herein means a material which is able to have lithium ions inserted therein and release lithium ion therefrom during repeated charging/discharging cycles.
There is no specific limitation to the silicon-based active material, and those which are known for use in lithium ion batteries may be used. In some examples, the silicon-based active material may be selected from the group consisting of silicon, silicon alloys and silicon/carbon composites. In some examples, the silicon alloy may comprise silicon and one or more metals selected from the group consisting of Ti, Sn, Al, Sb, Bi, As, Ge and Pb.
In some examples, the silicon-based active material may be in the form of powders, or may be ground into powders.
According to some examples of the present disclosure, the content of the silicon-based active material may be from 5% to 85% by weight, based on the total weight of the anode composition. For example, the content of the silicon-based active material may be about 5%, about 10%, about 15%, about 20%, about 25%, about 30%, about 35%, about 40%, about 45%, about 50%, about 55%, about 60%, about 65%, about 70, about 75%, about 80% and about 85% by weight, based on the total weight of the anode composition.
According to some examples of the present disclosure, the anode composition may comprise a carboxyl-containing binder.
There is no specific limitation to the carboxyl-containing binder, and those which are known for use in lithium ion batteries may be used. In some examples, the carboxyl-containing binder may be a carboxylic acid, or a mixture of a carboxylic acid and its alkali metal salt, wherein the carboxylic acid may be selected from the group consisting of polyacrylic acid (PAA), carboxymethyl cellulose, alginic acid and xanthan gum. In some examples, the alkali metal salt may be selected from the group consisting of a lithium salt, sodium salt and potassium salt.
According to some examples of the present disclosure, the content of the carboxyl-containing binder may be from 5% by weight to 25% by weight, for example, from 10% by weight to 20% by weight (e.g. about 10%, about 15% and about 20% by weight), based on the total weight of the anode composition.
According to some examples of the present disclosure, the anode composition may comprise a silane coupling agent represented by the following formula (1):
Y—(CH2)n—Si—X3 (1)
In the context of the present disclosure, the term “non-hydrolytic group” means a group that does not hydrolyze to form a hydroxyl group when being brought into contact with water or a water-containing solvent.
In the context of the present disclosure, the term “hydrolysable group” means a group that is capable of hydrolyzing to form a hydroxyl group when being brought into contact with water or a water-containing solvent.
In the context of the present disclosure, each of the terms “alkyl group”, “alkoxy group”, “alkenyl group” and “alkynyl group” may independently represent a linear, branched or cyclic group, and may independently contain from 1 to 12 carbon atoms, for example, from 1 to 10 carbon atoms, from 1 to 8 carbon atoms or from 1 to 4 carbon atoms.
In the context of the present disclosure, each of the terms “aromatic group” and “aroxy group” may independently contain from 6 to 12 carbon atoms, for example, contain 6, 7, 8, 9, 10, 11 or 12 carbon atoms.
In some examples, X may independently be a hydroxyl group. In some examples, X may independently be a halogen atom, such as a fluorine atom, a chlorine atom, a bromine atom or an iodine atom. In some examples, X may independently be an alkoxy group, wherein the alkoxy group may have the same definition as mentioned above. In some examples, X may independently be an ether group, for example, an ether group having a structure represented by —O(CH2)mOR′, wherein R′ may represent a hydrogen atom or an alkyl group, and the alkyl group may have the same definition as mentioned above; and m represents an integer from 0 to 4 (e.g., 0, 1, 2, 3 or 4). In some examples, X may independently be a siloxy group, for example, a siloxy group having a structure represented by —OSiRd3, wherein Rd each independently represents a hydrogen atom or an alkyl group, and the alkyl group may have the same definition as mentioned above. The three Rd groups in —OSiRd3 of the siloxy group may be identical with or different from each other.
In some examples, Y may comprise an aromatic conjugated moiety. In some examples, Y may be derived from aniline, pyrrole, thiophene and any combination thereof. In some examples, Y may be selected from the group consisting of
wherein * indicates the position where Y is linked to a moiety represented by —(CH2)n—Si—X3 in the silane coupling agent; Ra and Rb each independently represents a hydrogen atom, or a substituent selected from the group consisting of alkyl groups, alkoxy groups, alkenyl groups, alkynyl groups, aromatic groups and aroxy groups. In some examples, Y group in formula (1) may represent H and/or
and in these cases, Y may be abbreviated as an “aniline-derived moiety”. In order to allow the “aniline-derived moiety” in the silane coupling agent to polymerize as expected, it is preferred that the para-position to “—NH—” or “—NHRb” is occupied by hydrogen atom, rather than any substituent.
In some examples, Y group in formula (1) may represent
and in this case, Y may be abbreviated as a “pyrrole-derived moiety”. In some examples, Y group in formula (1) may represent
and in this case, Y may be abbreviated as a “thiophene-derived moiety”. In order to allow the “pyrrole-derived moiety” or “thiophene-derived moiety” in the silane coupling agent to polymerize as expected, it is preferred that the ortho-position to “—NH—” or to the sulfur atom is occupied by hydrogen atom, and a substituent (if any) may locate at a meta-position to “—NH—” or to the sulfur atom.
In the case where Y is
there may be one, two, three or four Ra groups altogether, and these Ra groups may be identical with or different from each other. In the case where Y is
there may be one, two or three Ra groups altogether, and these Ra groups may be identical with or different from each other.
In some examples, in formula (1), X each independently is an alkoxy group, and Y is
wherein the three X groups may be identical with or different from each other. In this case, the silane coupling agent may be represented by formula (2):
wherein Ra and n have the same definitions as those given for formula (1), Re each independently represents an alkyl group, the alkyl group may have the same definition as mentioned above, and the three Re groups may be identical with or different from each other.
Examples of the silane coupling agents represented by formula (2) may include, but not limited to, N-[(trimethoxysilyl)methyl]aniline, N-[(triethoxysilyl)methyl]aniline, N-[(trimethoxysilyl)ethyl]aniline, N-[(triethoxysilyl) ethyl]aniline, N-[3-(trimethoxysilyl)propyl]aniline and N-[3-(triethoxysilyl)propyl]aniline. For example, N-[(triethoxysilyl)methyl])aniline may be commercially available from Nanjing Diamond Chem Co. Ltd under the product name of ND42.
According to some examples of the present disclosure, the weight ratio of the silane coupling agent to the silicon-based active material may be no less than 0.01:100 but less than 3:100, for example, from 0.01:100 to 2.5:100, from 0.01:100 to 2:100, from 0.1:100 to 1:100, or being about 0.5:100.
Although not intended to be bound by theories, it is presumed that the following reaction mechanisms apply to the silane coupling agent, the silicon-based active material and the carboxyl-containing binder according to the present disclosure.
In the case where any one of the X groups in formula (1) represents a hydrolysable group, the hydrolysable group may hydrolyze upon contact with water or a water-containing solvent and thus form a hydroxyl group. The hydrolyzed product of the silane coupling agent may have a structure of silanol, for example, a completely hydrolyzed product of the silane coupling agent may be represented by Y—(CH2)n—Si—(OH)3.
In the case where all of the three X groups in formula (1) represent hydroxyl groups, the silane coupling agent may be represented by Y—(CH2)n—Si—(OH)3, therefore, the hydrolysis of the silane coupling agent may be omitted.
Since silicon has a high affinity for oxygen, an oxide layer will spontaneously form on the surface of silicon upon exposure to air even at room temperature. Therefore, there is usually a natural silicon oxide layer on the surface of the silicon-based active material. The surface layer of silicon oxide contains hydroxyl groups, i.e., silanol groups —Si—OH.
The hydroxyl groups contained in the hydrolyzed silane coupling agent (e.g., Y—(CH2)n—Si—(OH)3) may condense with the hydroxyl groups on the surface of the silicon-based active material, with a water molecule being eliminated.
Condensation may also occur between the Si—OH groups in adjacent hydrolyzed silane coupling agents (e.g., Y—(CH2)n—Si—(OH)3) per se, which enhances the crosslinking degree of the final polymerized product as mentioned below.
iii) Formation of a Conductive Polymer Moiety by Polymerization of the Aromatic Conjugated Moiety in the Silane Coupling Agent
The aromatic conjugated moiety (i.e., the Y group), such as the aniline-derived moiety, pyrrole-derived moiety and thiophene-derived moiety in the silane coupling agent may readily form an electrically conductive polymer moiety upon polymerization, and thus improve the electron conductivity and charge/discharge capacity of the whole anode, especially at high current density. The polymerization may be conducted by employing an oxidizing agent, or by exposing the silane coupling agent to ultraviolet irradiation and/or microwave irradiation.
On the one hand, the —NH— group in the polyaniline moiety and polypyrrole moiety may react with the carboxyl group in the carboxyl-containing binder to form an amido group by eliminating a water molecule.
On the other hand, under an acidic condition provided by the carboxyl-containing binder, the π-conjugated system of the polyaniline moiety, polypyrrole moiety and the polythiophene moiety in the polymerized silane coupling agent may remove an electron to form a cation, which may also be referred to as “p-doping”. Meanwhile, the carboxyl-containing binder may accept an electron to form an anion. The cation and the anion thus generated may electrostatically combine together to form a salt.
For example, the polyaniline moiety may be p-doped and converted into a structure represented by
The polypyrrole moiety may be p-doped and converted into a structure represented by
The polythiophene moiety may be p-doped and converted into a structure represented by
Herein, the wavy line “” indicates the position where the p-doped polyaniline moiety, polypyrrole moiety or the polythiophene moiety is linked to the rest of the polymerized silane coupling agents. “⊕” indicates a p-doped position in the polyaniline moiety, polypyrrole moiety or the polythiophene moiety. “A−” represents an anion obtained from the carboxyl-containing binder by accepting an electron. Therefore, the polymerized and p-doped silane coupling agent may electrostatically connect with the carboxyl-containing binder.
Comparing with the anode composition shown in
In contrast, when employing a silane coupling agent (such as KH-550, i.e. γ-aminopropyl triethoxysilane (NH2C3H6Si(OC2H5)3) that contains an aliphatic amino group or aliphatic imino group, but does not contain an aromatic conjugated moiety (such as a aniline-derived moiety, pyrrole-derived moiety and thiophene-derived moiety), an electronically insulative network is formed, which inhibits electron transmission and hinders the electrochemical activity of the silicon-based active material, and leads to a poor rate performance.
Therefore, the anode composition according to the present disclosure may impart excellent electrochemical properties, especially excellent cycling stability and rate performance to lithium ion batteries.
According to some examples of the present disclosure, the anode composition may optionally comprise a carbon material. The carbon material may increase the conductivity and/or capacity of the anode.
There is no specific limitation to the carbon material, and those which are known for use in lithium ion batteries may be used. In some examples, the carbon material may be selected from the group consisting of carbon black, super P, acetylene black, Ketjen black, graphite, graphene, carbon nanotubes and vapour grown carbon fibers. For example, super P may be commercially available from Timical.
In some examples, the carbon material may be in the form of powders, or may be ground into powders.
According to some examples of the present disclosure, the content of the carbon material may be from 0% by weight to 80% by weight, for example, from 5% by weight to 80% or from 20% by weight to 60% by weight, based on the total weight of the anode composition.
According to some examples of the present disclosure, the anode composition may optionally comprise component e): a chain extender. The chain extender may copolymerize with the aromatic conjugated moiety of the silane coupling agent, thereby allowing the polymer chain to propagate and enhance the electron conductivity of the whole anode.
In some examples, the chain extender may be selected from the group consisting of aniline, pyrrole, thiophene and their derivatives. In some examples, the chain extender corresponds to the aromatic conjugated moiety of the silane coupling agent. For example, in the case where an “aniline-derived moiety” is contained in the silane coupling agent, aniline or its derivative may be employed as chain extender. In the case where a “pyrrole-derived moiety” is contained in the silane coupling agent, pyrrole or its derivative may be employed as chain extender. In the case where a “thiophene-derived moiety” is contained in the silane coupling agent, thiophene or its derivative may be employed as chain extender.
According to some examples of the present disclosure, the content of the chain extender may be from 0 to 30% by weight, for example, about 5%, about 10%, about 15%, about 20%, about 25 or about 35%, based on the total weight of the anode composition.
There is no specific limitation to the preparation process of the anode. In some examples, the process for preparing an anode may comprise:
The term “water-containing solvent” as used in this disclosure means a solvent mixture contains water and a solvent other than water, such as a mixture of water and an alcohol.
In some examples, the polymerization is conducted by employing an oxidizing agent, or exposing the slurry to ultraviolet irradiation and/or microwave irradiation.
In some examples, the oxidizing agent may be selected from the group consisting of ammonium persulfate ((NH4)2S2O8), iron (III) chloride, copper (II) chloride, silver nitrate, hydrogen peroxide, chloroauric acid and ammonium cerium (IV) nitrate. For example, (NH4)2S2O8 may be commercially available from Sinopharm Chemical Reagent Co., Ltd. The oxidizing agent may also be removed, physically and/or chemically, after the silane coupling agent is polymerized.
In the case where an oxidizing agent is used, it may not only initiate the polymerization of the silane coupling agent, but also initiate the copolymerization of the chain extender (if any) with the silane coupling agent. The total amount of the oxidizing agent to be used is the sum of the amount of the oxidizing agent which the silane coupling agent needs to polymerize and the amount of the oxidizing agent which the chain extender (if any) needs to copolymerize. In some examples, the weight ratio of the silane coupling agent to the oxidizing agent needed by the silane coupling agent may vary from 1:1 to 4:1, for example, 1:1, 2:1, 3:1 or 4:1; and the weight ratio of the chain extender to the oxidizing agent needed by the chain extender is from 4:1 to 1:4, for example, 4:1, 3:1, 2:1 or 1:1.
The lithium ion battery according to the present invention may comprise an anode prepared from the anode composition according to the present disclosure, or comprising an anode prepared by the process according to the present disclosure.
The lithium ion batteries according to the present disclosure may be used in energy storage systems and electric vehicles.
In general, when the cathode efficiency is higher than the anode efficiency, a prelithiation can effectively increase the cell capacity via increasing the initial Coulombic efficiency. In this case, maximum energy density can be reached. For a cell, in which the loss of lithium during cycling may occur, prelithiation can also improve the cycling performance when an over-prelithiation is applied. The over-prelithiation provides a reservoir of lithium in the whole electrochemical system and the extra lithium in the anode compensates the possible lithium consumption from the cathode during cycling.
In principle, the higher prelithiation degree, the better cycling performance could be achieved. However, a higher prelithiation degree involves a much larger anode.
Therefore, the cell energy density will decrease due to the increased weight and volume of the anode. Therefore, the prelithiation degree should be carefully controlled to balance the cycling performance and the energy density.
The present invention, according to one aspect, relates to a lithium-ion battery comprising a cathode, an electrolyte, and an anode, wherein the anode is prepared from the anode composition according to the present disclosure, or prepared by the process according to the present disclosure, and the initial surface capacity a of the cathode and the initial surface capacity b of the anode satisfy the relation formulae
1<(b·(1−ε)/a)≤1.2 (I),
0<ε≤((a·η1)/0.6−(a−b·(1−η2)))/b (II),
where
ε is the prelithiation degree of the anode,
η1 is the initial coulombic efficiency of the cathode, and
η2 is the initial coulombic efficiency of the anode.
In the context of the present invention, the term “surface capacity” means the specific surface capacity in mAh/cm2, the electrode capacity per unit of the electrode surface area. The term “initial capacity of the cathode” means the initial delithiation capacity of the cathode, and the term “initial capacity of the anode” means the initial lithiation capacity of the anode.
According to the present invention, the term “prelithiation degree” ε of the anode can be calculated by (b−a·x)/b, wherein x is the balance of the anode capacity after prelithiation and the cathode capacity. For safety reasons, the anode capacity is usually designed slightly greater than the cathode capacity, and the balance of the anode capacity after prelithiation and the cathode capacity can be selected from greater than 1 to 1.2, preferably from 1.05 to 1.15, more preferably from 1.08 to 1.12, particular preferably about 1.1.
In accordance with an embodiment of the lithium-ion battery according to the present invention, the initial surface capacity a of the cathode and the initial surface capacity b of the anode satisfy the relation formulae
1.05≤(b·(1−ε)/a)≤1.15 (Ia),
preferably 1.08≤(b·(1−ε)/a)≤1.12 (Ib).
In accordance with another embodiment of the lithium-ion battery according to the present invention, the prelithiation degree of the anode can be defined as
ε=((a·η1)/c−(a−b·(1−η2)))/b (III),
0.6≤c<1 (IV),
preferably 0.7≤c<1 (IVa),
more preferably 0.7≤c≤0.9 (IVb),
particular preferably 0.75≤c≤0.85 (IVc),
where
c is the depth of discharge (DoD) of the anode.
In particular, ε=(b·(1−η2)−a·(1−η1))/b, when c=1.
In accordance with another embodiment of the lithium-ion battery according to the present invention, the active material of the anode can be selected from the group consisting of carbon, silicon, silicon intermetallic compound, silicon oxide, silicon alloy and mixtures thereof.
In accordance with another embodiment of the lithium-ion battery according to the present invention, the active material of the cathode can be selected from the group consisting of lithium nickel oxide, lithium cobalt oxide, lithium manganese oxide, lithium nickel cobalt oxide, lithium nickel cobalt manganese oxide, and mixtures thereof.
The present invention, according to another aspect, relates to a method for producing a lithium-ion battery comprising a cathode, an electrolyte, and an anode, wherein the anode is prepared from the anode composition according to the present disclosure, or prepared by the process according to the present disclosure, and said method includes the following steps:
1<(b·(1−ε)/a)≤1.2 (I),
0<ε≤((a·η1)/0.6−(a−b·(1−η2)))/b (II),
where
ε is the prelithiation degree of the anode,
η1 is the initial coulombic efficiency of the cathode, and
η2 is the initial coulombic efficiency of the anode.
In the context of the present invention, the term “surface capacity” means the specific surface capacity in mAh/cm2, the electrode capacity per unit of the electrode surface area. The term “initial capacity of the cathode” means the initial delithiation capacity of the cathode, and the term “initial capacity of the anode” means the initial lithiation capacity of the anode.
According to the present invention, the term “prelithiation degree” ε of the anode can be calculated by (b−a·x)/b, wherein x is the balance of the anode capacity after prelithiation and the cathode capacity. For safety reasons, the anode capacity is usually designed slightly greater than the cathode capacity, and the balance of the anode capacity after prelithiation and the cathode capacity can be selected from greater than 1 to 1.2, preferably from 1.05 to 1.15, more preferably from 1.08 to 1.12, particular preferably about 1.1.
The prelithiation process is not particularly limited. The lithiation of the anode active material substrate can be carried out for example in several different ways. A physical process includes deposition of a lithium coating layer on the surface of the anode active material substrate such as silicon particles, thermally induced diffusion of lithium into the substrate such as silicon particles, or spray of stabilized Li powder onto the anode tape. An electrochemical process includes using silicon particles and a lithium metal plate as the electrodes, and applying an electrochemical potential so as to intercalate Li+ ions into the bulk of the silicon particles. An alternative electrochemical process includes assembling a half cell with silicon particles and Li metal foil electrodes, charging the half cell, and disassembling the half cell to obtain lithiated silicon particles.
In accordance with an embodiment of the method according to the present invention, the initial surface capacity a of the cathode and the initial surface capacity b of the anode satisfy the relation formulae
1.05≤(b·(1−ε)/a)≤1.15 (Ia),
preferably 1.08≤(b·(1−ε)/a)≤1.12 (Ib).
In accordance with another embodiment of the method according to the present invention, the prelithiation degree of the anode can be defined as
ε=((a·η1)/c−(a−b·(1−η2)))/b (III),
0.6≤c<1 (IV),
preferably 0.7≤c<1 (IVa),
more preferably 0.7≤c≤0.9 (IVb),
particular preferably 0.75≤c≤0.85 (IVc),
where
c is the depth of discharge (DoD) of the anode.
In particular, ε=(b·(1−η2)−a·(1−η1))/b, when c=1.
In accordance with another embodiment of the method according to the present invention, the active material of the anode can be selected from the group consisting of carbon, silicon, silicon intermetallic compound, silicon oxide, silicon alloy and mixtures thereof.
In accordance with another embodiment of the method according to the present invention, the active material of the cathode can be selected from the group consisting of lithium nickel oxide, lithium cobalt oxide, lithium manganese oxide, lithium nickel cobalt oxide, lithium nickel cobalt manganese oxide, and mixtures thereof.
Prior art prelithiation methods often involve a treatment of coated anode tape. This could be an electrochemical process, or physical contact of the anode with stabilized lithium metal powder. However, these prelithiation procedure requires additional steps to the current battery production method. Furthermore, due to the highly active nature of the prelithiated anode, the subsequent battery production procedure requires an environment with well-controlled humidity, which results in an increased cost for the cell production.
The present invention provides an alternative method of in-situ prelithiation. The lithium source for prelithaition comes from the cathode. During the first formation cycle, by increasing the cut-off voltage of the full cell, additional amount of lithium is extracted from the cathode; by controlling the discharge capacity, the additional lithium extracted from the cathode is stored at the anode, and this is ensured in the following cycles by maintaining the upper cut-off voltage the same as in the first cycle.
The present invention, according to another aspect, relates to a lithium-ion battery comprising a cathode, an electrolyte, and an anode, characterized in that the anode is prepared from the anode composition according to the present disclosure, or prepared by the process according to the present disclosure, and said lithium-ion battery is subjected to a formation process, wherein said formation process includes an initial formation cycle comprising the following steps:
In the context of the present invention, the term “formation process” means the initial one or more charging/discharging cycles of the lithium-ion battery for example at 0.1C, once the lithium-ion battery is assembled. During this process, a stable solid-electrolyte-inter-phase (SEI) layer can be formed at the anode.
In accordance with an embodiment of the formation process according to the present invention, in step a) the battery can be charged to a cut off voltage which is up to 0.8 V greater than the nominal charge cut off voltage of the battery, preferably 0.1˜0.5 V greater than the nominal charge cut off voltage of the battery, more preferably 0.2˜0.4 V greater than the nominal charge cut off voltage of the battery, particular preferably about 0.3 V greater than the nominal charge cut off voltage of the battery.
A lithium-ion battery with the typical cathode materials of cobalt, nickel, manganese and aluminum typically charges to 4.20V±50 mV as the nominal charge cut off voltage. Some nickel-based batteries charge to 4.10V±50 mV.
In accordance with another embodiment of the formation process according to the present invention, the nominal charge cut off voltage of the battery can be about 4.2 V±50 mV, and the nominal discharge cut off voltage of the battery can be about 2.5 V±50 mV.
In accordance with another embodiment of the formation process according to the present invention, the Coulombic efficiency of the cathode in the initial formation cycle can be 40%˜80%, preferably 50%˜70%.
In accordance with another embodiment of the formation process according to the present invention, said formation process further includes one or two or more formation cycles, which are carried out in the same way as the initial formation cycle.
For the traditional lithium-ion batteries, when the battery is charged to a cut off voltage greater than the nominal charge cut off voltage, metallic lithium will be plated on the anode, the cathode material becomes an oxidizing agent, produces carbon dioxide (CO2), and increases the battery pressure.
In case of a preferred lithium-ion battery defined below according to the present invention, when the battery is charged to a cut off voltage greater than the nominal charge cut off voltage, additional Li+ ions can be intercalated into the anode having additional capacity, instead of being plated on the anode.
In case of another preferred lithium-ion battery defined below according to the present invention, in which the electrolyte comprises one or more fluorinated carbonate compounds as a nonaqueous organic solvent, the electrochemical window of the electrolyte can be broadened, and the safety of the battery can still be ensured at a charge cut off voltage of 5V or even higher.
In order to implement the present invention, an additional cathode capacity can preferably be supplemented to the nominal initial surface capacity of the cathode.
In the context of the present invention, the term “nominal initial surface capacity” a of the cathode means the nominally designed initial surface capacity of the cathode.
In the context of the present invention, the term “surface capacity” means the specific surface capacity in mAh/cm2, the electrode capacity per unit of the electrode surface area. The term “initial capacity of the cathode” means the initial delithiation capacity of the cathode, and the term “initial capacity of the anode” means the initial lithiation capacity of the anode.
In accordance with an embodiment of the lithium-ion battery according to the present invention, the relative increment r of the initial surface capacity of the cathode over the nominal initial surface capacity a of the cathode and the cut off voltage Voff satisfy the following linear equation with a tolerance of ±5%, ±10%, or ±20%
r=−0.75Voff−3.134 (V).
In accordance with another embodiment of the lithium-ion battery according to the present invention, the relative increment r of the initial surface capacity of the cathode over the nominal initial surface capacity a of the cathode and the cut off voltage Voff satisfy the following quadratic equation with a tolerance of ±5%, ±10%, or ±20%
r=−0.7857Voff2+7.6643Voff−18.33 (Va).
In accordance with another embodiment of the lithium-ion battery according to the present invention, the nominal initial surface capacity a of the cathode and the initial surface capacity b of the anode satisfy the relation formulae
1<b·η2/(a·(1+r)−b·(1−η2))−ε≤1.2 (I′),
preferably 1.05≤b·η2/(a·(1+r)−b·(1−η2))−ε≤1.15 (Ia′),
more preferably 1.08≤b·η2/(a·(1+r)−b·(1−η2))−ε≤1.12 (Ib′),
0<ε≤((a·η1)/0.6−(a−b·(1−η2)))/b (II),
where
ε is the prelithiation degree of the anode, and
η2 is the initial coulombic efficiency of the anode.
According to the present invention, the term “prelithiation degree” ε of the anode can be calculated by (b−a·x)/b, wherein x is the balance of the anode capacity after prelithiation and the cathode capacity. For safety reasons, the anode capacity is usually designed slightly greater than the cathode capacity, and the balance of the anode capacity after prelithiation and the cathode capacity can be selected from greater than 1 to 1.2, preferably from 1.05 to 1.15, more preferably from 1.08 to 1.12, particular preferably about 1.1.
In accordance with another embodiment of the lithium-ion battery according to the present invention, the prelithiation degree of the anode can be defined as
ε=((a·η1)/c−(a−b·(1−η2)))/b (III),
0.6≤c<1 (IV),
preferably 0.7≤c<1 (IVa),
more preferably 0.7≤c≤0.9 (IVb),
particular preferably 0.75≤c≤0.85 (IVc),
where
η1 is the initial coulombic efficiency of the cathode, and
c is the depth of discharge (DoD) of the anode.
In particular, ε=(b·(1−η2)−a·(1−η1))/b, when c=1.
In accordance with another embodiment of the lithium-ion battery according to the present invention, the electrolyte comprises one or more fluorinated carbonate compounds, preferably fluorinated cyclic or acyclic carbonate compounds, as a nonaqueous organic solvent.
In accordance with another embodiment of the lithium-ion battery according to the present invention, the fluorinated carbonate compounds can be selected from the group consisting of fluorinated ethylene carbonate, fluorinated propylene carbonate, fluorinated dimethyl carbonate, fluorinated methyl ethyl carbonate, and fluorinated diethyl carbonate, in which the “fluorinated” carbonate compounds can be understood as “monofluorinated”, “difluorinated”, “trifluorinated”, “tetrafluorinated”, and “perfluorinated” carbonate compounds.
In accordance with another embodiment of the lithium-ion battery according to the present invention, the fluorinated carbonate compounds can be selected from the group consisting of monofluoroethylene carbonate, 4,4-difluoro ethylene carbonate, 4,5-difluoro ethylene carbonate, 4,4,5-trifluoroethylene carbonate, 4,4,5,5-tetrafluoroethylene carbonate, 4-fluoro-4-methyl ethylene carbonate, 4,5-difluoro-4-methyl ethylene carbonate, 4-fluoro-5-methyl ethylene carbonate, 4,4-difluoro-5-methyl ethylene carbonate, 4-(fluoromethyl)-ethylene carbonate, 4-(difluoromethyl)-ethylene carbonate, 4-(trifluoromethyl)-ethylene carbonate, 4-(fluoromethyl)-4-fluoro ethylene carbonate, 4-(fluoromethyl)-5-fluoro ethylene carbonate, 4,4,5-trifluoro-5-methyl ethylene carbonate, 4-fluoro-4,5-dimethyl ethylene carbonate, 4,5-difluoro-4,5-dimethyl ethylene carbonate, and 4,4-difluoro-5,5-dimethyl ethylene carbonate.
In accordance with another embodiment of the lithium-ion battery according to the present invention, the content of the fluorinated carbonate compounds can be 10˜100 vol. %, preferably 30˜100 vol. %, more preferably 50˜100 vol. %, particular preferably 80˜100 vol. %, based on the total nonaqueous organic solvent.
In accordance with another embodiment of the lithium-ion battery according to the present invention, the active material of the anode can be selected from the group consisting of carbon, silicon, silicon intermetallic compound, silicon oxide, silicon alloy and mixtures thereof.
In accordance with another embodiment of the lithium-ion battery according to the present invention, the active material of the cathode can be selected from the group consisting of lithium nickel oxide, lithium cobalt oxide, lithium manganese oxide, lithium nickel cobalt oxide, lithium nickel cobalt manganese oxide, and mixtures thereof.
In accordance with another embodiment of the lithium-ion battery according to the present invention, after being subjected to the formation process, said lithium-ion battery can still be charged to a cut off voltage Voff, which is greater than the nominal charge cut off voltage of the battery, and be discharged to the nominal discharge cut off voltage of the battery.
In accordance with another embodiment of the lithium-ion battery according to the present invention, after being subjected to the formation process, said lithium-ion battery can still be charged to a cut off voltage Voff, which is up to 0.8 V greater than the nominal charge cut off voltage of the battery, more preferably 0.1˜0.5 V greater than the nominal charge cut off voltage of the battery, particular preferably 0.2˜0.4 V greater than the nominal charge cut off voltage of the battery, especially preferably about 0.3 V greater than the nominal charge cut off voltage of the battery, and be discharged to the nominal discharge cut off voltage of the battery.
The present invention, according to another aspect, relates to a method for producing a lithium-ion battery comprising a cathode, an electrolyte, and an anode, wherein the anode is prepared from the anode composition according to the present disclosure, or prepared by the process according to the present disclosure, and said method includes the following steps:
In the context of the present invention, the term “formation process” means the initial one or more charging/discharging cycles of the lithium-ion battery for example at 0.1C, once the lithium-ion battery is assembled. During this process, a stable solid-electrolyte-inter-phase (SEI) layer can be formed at the anode.
In accordance with an embodiment of the formation process according to the present invention, in step a) the battery can be charged to a cut off voltage which is up to 0.8 V greater than the nominal charge cut off voltage of the battery, preferably 0.1˜0.5 V greater than the nominal charge cut off voltage of the battery, more preferably 0.2˜0.4 V greater than the nominal charge cut off voltage of the battery, particular preferably about 0.3 V greater than the nominal charge cut off voltage of the battery.
A lithium-ion battery with the typical cathode materials of cobalt, nickel, manganese and aluminum typically charges to 4.20V±50 mV as the nominal charge cut off voltage. Some nickel-based batteries charge to 4.10V±50 mV.
In accordance with another embodiment of the formation process according to the present invention, the nominal charge cut off voltage of the battery can be about 4.2 V±50 mV, and the nominal discharge cut off voltage of the battery can be about 2.5 V±50 mV.
In accordance with another embodiment of the formation process according to the present invention, the Coulombic efficiency of the cathode in the initial formation cycle can be 40%˜80%, preferably 50%˜70%.
In accordance with another embodiment of the formation process according to the present invention, said formation process further includes one or two or more formation cycles, which are carried out in the same way as the initial formation cycle.
In order to implement the present invention, an additional cathode capacity can preferably be supplemented to the nominal initial surface capacity of the cathode.
In the context of the present invention, the term “nominal initial surface capacity” a of the cathode means the nominally designed initial surface capacity of the cathode.
In the context of the present invention, the term “surface capacity” means the specific surface capacity in mAh/cm2, the electrode capacity per unit of the electrode surface area. The term “initial capacity of the cathode” means the initial delithiation capacity of the cathode, and the term “initial capacity of the anode” means the initial lithiation capacity of the anode.
In accordance with an embodiment of the method according to the present invention, the relative increment r of the initial surface capacity of the cathode over the nominal initial surface capacity a of the cathode and the cut off voltage Voff satisfy the following linear equation with a tolerance of ±5%, ±10%, or ±20%
r=−0.75Voff−3.134 (V).
In accordance with another embodiment of the method according to the present invention, the relative increment r of the initial surface capacity of the cathode over the nominal initial surface capacity a of the cathode and the cut off voltage Voff satisfy the following quadratic equation with a tolerance of ±5%, ±10%, or ±20%
r=−0.7857Voff2+7.6643Voff−18.33 (Va).
In accordance with another embodiment of the method according to the present invention, the nominal initial surface capacity a of the cathode and the initial surface capacity b of the anode satisfy the relation formulae
1<b·η2/(a·(1+r)−b·(1−η2))−ε≤1.2 (I′),
preferably 1.05≤b·η2/(a·(1+r)−b·(1−η2))−ε≤1.15 (Ia′),
more preferably 1.08≤b·η2/(a·(1+r)−b·(1−η2))−ε≤1.12 (Ib′),
0<ε≤((a·η1)/0.6−(a−b·(1−η2)))/b (II),
where
ε is the prelithiation degree of the anode, and
η2 is the initial coulombic efficiency of the anode.
According to the present invention, the term “prelithiation degree” ε of the anode can be calculated by (b−a·x)/b, wherein x is the balance of the anode capacity after prelithiation and the cathode capacity. For safety reasons, the anode capacity is usually designed slightly greater than the cathode capacity, and the balance of the anode capacity after prelithiation and the cathode capacity can be selected from greater than 1 to 1.2, preferably from 1.05 to 1.15, more preferably from 1.08 to 1.12, particular preferably about 1.1.
In accordance with another embodiment of the method according to the present invention, the prelithiation degree of the anode can be defined as
ε=((a·η1)/c−(a−b·(1−η2)))/b (III),
0.6≤c<1 (IV),
preferably 0.7≤c<1 (IVa),
more preferably 0.7≤c≤0.9 (IVb),
particular preferably 0.75≤c≤0.85 (IVc),
where
η1 is the initial coulombic efficiency of the cathode, and
c is the depth of discharge (DoD) of the anode.
In particular, c=(b·(1−η2)−a·(1−η1))/b, when c=1.
In accordance with another embodiment of the method according to the present invention, the electrolyte comprises one or more fluorinated carbonate compounds, preferably fluorinated cyclic or acyclic carbonate compounds, as a nonaqueous organic solvent.
In accordance with another embodiment of the method according to the present invention, the fluorinated carbonate compounds can be selected from the group consisting of fluorinated ethylene carbonate, fluorinated propylene carbonate, fluorinated dimethyl carbonate, fluorinated methyl ethyl carbonate, and fluorinated diethyl carbonate, in which the “fluorinated” carbonate compounds can be understood as “monofluorinated”, “difluorinated”, “trifluorinated”, “tetrafluorinated”, and “perfluorinated” carbonate compounds.
In accordance with another embodiment of the method according to the present invention, the fluorinated carbonate compounds can be selected from the group consisting of monofluoroethylene carbonate, 4,4-difluoro ethylene carbonate, 4,5-difluoro ethylene carbonate, 4,4,5-trifluoroethylene carbonate, 4,4,5,5-tetrafluoroethylene carbonate, 4-fluoro-4-methyl ethylene carbonate, 4,5-difluoro-4-methyl ethylene carbonate, 4-fluoro-5-methyl ethylene carbonate, 4,4-difluoro-5-methyl ethylene carbonate, 4-(fluoromethyl)-ethylene carbonate, 4-(difluoromethyl)-ethylene carbonate, 4-(trifluoromethyl)-ethylene carbonate, 4-(fluoromethyl)-4-fluoro ethylene carbonate, 4-(fluoromethyl)-5-fluoro ethylene carbonate, 4,4,5-trifluoro-5-methyl ethylene carbonate, 4-fluoro-4,5-dimethyl ethylene carbonate, 4,5-difluoro-4,5-dimethyl ethylene carbonate, and 4,4-difluoro-5,5-dimethyl ethylene carbonate.
In accordance with another embodiment of the method according to the present invention, the content of the fluorinated carbonate compounds can be 10˜100 vol. %, preferably 30˜100 vol. %, more preferably 50˜100 vol. %, particular preferably 80˜100 vol. %, based on the total nonaqueous organic solvent.
In accordance with another embodiment of the method according to the present invention, the active material of the anode can be selected from the group consisting of carbon, silicon, silicon intermetallic compound, silicon oxide, silicon alloy and mixtures thereof.
In accordance with another embodiment of the method according to the present invention, the active material of the cathode can be selected from the group consisting of lithium nickel oxide, lithium cobalt oxide, lithium manganese oxide, lithium nickel cobalt oxide, lithium nickel cobalt manganese oxide, and mixtures thereof.
Nano silicon particles: silicon-based active material, 50-200 nm, available from Alfa-Aesar.
Super P: carbon material, 40 nm, available from Timical.
PAA: polyacrylic acid, binder, Mv: ˜450 000, available from Aldrich.
ND42: N-[(triethoxysilyl)methyl])aniline, silane coupling agent containing an aromatic conjugated moiety, available from Nanjing Diamond Chem Co., Ltd.
KH550: γ-aminopropyl triethoxysilane, silane coupling agent containing no aromatic conjugated moiety, available from Sinopharm Chemical Reagent Co. Ltd.
(NH4)2S2O8: oxidizing agent, available from Sinopharm Chemical Reagent Co., Ltd.
Aniline: chain extender, available from Sinopharm Chemical Reagent Co. Ltd.
ET20-26: polyethylene (PE), separator, available from ENTEK.
800 mg nano silicon particles were mixed with 100 mg Super P and 100 mg PAA in water to obtain a mixture. After stirring for 1 h, 4 mg ND42 was added into the mixture. Subsequently, the mixture was stirred for another 4 h, then 2 mg (NH4)2S2O8 was added into the mixture. After stirring for another 1 h, the resultant slurry was coated on a Cu foil, then dried at 70° C. in vacuum for 8 h. The coated Cu foil was cut into several Φ 12 mm anodes. Considering that the weight ratio of the silane coupling agent (ND 42) to the nano silicon particles was 0.5:100, the anode obtained from Example 1 is abbreviated to Si—0.5% ND42-PAA.
A coin cell (CR2016) was assembled in an Argon-filled glovebox (MB-10 compact, MBraun) by using the anode obtained above. A Li metal foil was used as a counter electrode. 1M LiPF6 in FEC/EC/DMC (1:5:5 by volume, a mixture of fluoroethylene carbonate (FEC), ethylene carbonate (EC) and dimethyl carbonate (DMC)) was used as an electrolyte. ET20-26 was employed as a separator.
A cell was prepared in the same way as described above for Example 1, except that 8 mg ND42 was used instead of 4 mg ND42 and 4 mg (NH4)2S2O8 was used instead of 2 mg (NH4)2S2O8. Considering that the weight ratio of the silane coupling agent (ND 42) to the nano silicon particles was 1:100, the anode obtained from Example 2 is abbreviated to Si-1% ND42-PAA.
A cell was prepared in the same way as described above for Example 1, except that 0.8 mg ND42 was used instead of 4 mg ND42 and 0.4 mg (NH4)2S2O8 was used instead of 2 mg (NH4)2S2O8. Considering that the weight ratio of the silane coupling agent (ND 42) to the nano silicon particles was 0.1:100, the anode obtained from Example 3 is abbreviated to Si—0.1% ND42-PAA.
A cell was prepared in the same way as described above for Example 1, except that 24 mg aniline was additionally added during preparation of the anode and 26 mg (NH4)2S2O8 was used instead of 2 mg (NH4)2S2O8. Here, 26 mg (NH4)2S2O8 was the sum of 2 mg (NH4)2S2O8 needed by ND42 and 24 mg (NH4)2S2O8 needed by aniline. Considering that the aniline copolymerized with ND42 to form a polyaniline (PANI)-ND42 copolymer, and that the weight ratio of the silane coupling agent (ND42): aniline: nano silicon particles was 0.5:3:100, the anode obtained from Example 4 is abbreviated to Si—0.5% ND42-3% PANI-PAA.
A cell was prepared in the same way as described above for Example 1, except that 4 mg KH550 was used instead of 4 mg ND42, and no (NH4)2S2O8 was used. Considering that the weight ratio of the silane coupling agent (KH550) to the nano silicon particles was 0.5:100, the anode obtained from Comparative Example 1 is abbreviated to Si—0.5% KH550-PAA.
A cell was prepared in the same way as described above for Example 1, except that neither silane coupling agent nor (NH4)2S2O8 was used. Hereinafter, the anode obtained from Comparative Example 2 is abbreviated to Si-PAA.
A cell was prepared in the same way as described above for Example 1, except that 24 mg ND42 was used instead of 4 mg ND42 and 12 mg (NH4)2S2O8 was used instead of 2 mg (NH4)2S2O8. Considering that the weight ratio of the silane coupling agent ND 42 to the nano silicon particles was 3:100, the anode obtained from Comparative Example 3 is abbreviated to Si-3% ND42-PAA.
The cycling performance of each cell was evaluated on a LAND battery test system (Wuhan Kingnuo Electronics Co., Ltd., China) at 25° C. Each cell was discharged/charged within a voltage range of from 0.01 to 1.2V (vs Li/Li+) and at 0.1 A g−1 for the 1st cycle, at 0.3 A g−1 for the 2nd and 3rd cycles, and at a constant current density of 1.5 A g−1 for the following cycles. The mass loading of the nano silicon particles in each anode of the cells is about 0.5 mg/cm2.
The rate performance of each cell was evaluated on a LAND battery test system (Wuhan Kingnuo Electronics Co., Ltd., China) at 25° C. Each cell was discharged/charged within the voltage range of from 0.01 to 1.2V (vs Li/Li+) at a constant current density of 1.5 A g−1.
By referring to
At first anode/Li half cells were assembled in form of 2016 coin cell in an Argon-filled glove box (MB-10 compact, MBraun), wherein lithium metal was used as the counter electrode. The assembled anode/Li half cells were discharged to the designed prelithiation degree ε as given in Table P1-E1, so as to put a certain amount of Li+ ions in the anode, i.e., the prelithiation of the anode. Then the half cells were disassembled. The prelithiated anode and NCM-111 cathode were assembled to obtain 2032 coin full cells. The cycling performances of the full cells were evaluated at 25° C. on an Arbin battery test system at 0.1C for formation and at 1C for cycling.
In case of Group G0 with a prelithiation degree E=0, the capacity of the full cell was decreased to 80% after 339 cycles.
In case of Group G1 with a prelithiation degree of 5.6%, the prelithiation amount was only enough to compensate the irreversible Li loss difference between the cathode and the anode. Therefore, the initial Coulombic efficiency was increased from 83% to 86%, while no obvious improvement in cycling performance was observed.
In case of Group G2 with a prelithiation degree increased to 19.5%, the prelithiation amount was not only enough to compensate the irreversible Li loss difference between the cathode and the anode, but also extra amount of Li was reserved in the anode to compensate the Li loss during cycling. Hence, the cycle life was greatly improved to 616 cycles.
In case of Groups G3 and G4 with further increased prelithiation degrees, more and more Li was reserved in the anode, so better and better cycling performances were obtained.
Compared with non-prelithiation (G0), Group G1 with 5.6% prelithiation degree shows a higher energy density due to the higher capacity. In case of the further increased prelithiation degree for a better cycling performance, the energy density decreases to some extend but still has more than 90% energy density of G0 when prelithiation degree reaches 34.6% in G4.
Example P1-E2 was carried out similar to Example P1-E1, except that HE-NCM was used as the cathode active material and the corresponding parameters were given in Table P1-E2.
Example P1-E3 was carried out similar to Example P1-E1, except that pouch cells were assembled instead of coin cells, and the corresponding prelithiation degrees ε of the anode were a) 0 and b) 22%.
A pouch cell was assembled with a cathode initial capacity of 3.83 mAh/cm2 and an anode initial capacity of 4.36 mAh/cm2 in an Argon-filled glove box (MB-10 compact, MBraun). The cycling performance was evaluated at 25° C. on an Arbin battery test system at 0.1C for formation and at 1C for cycling, wherein the cell was charged to the nominal charge cut off voltage 4.2 V, and discharged to the nominal discharge cut off voltage 2.5 V or to a cut off capacity of 3.1 mAh/cm2. The calculated prelithiation degree ε of the anode was 0.
A pouch cell was assembled with a cathode initial capacity of 3.73 mAh/cm2 and an anode initial capacity of 5.17 mAh/cm2 in an Argon-filled glove box (MB-10 compact, MBraun). The cycling performance was evaluated at 25° C. on an Arbin battery test system at 0.1C for formation and at 1C for cycling, wherein the cell was charged to a cut off voltage of 4.5 V, which was 0.3 V greater than the nominal charge cut off voltage, and discharged to the nominal discharge cut off voltage 2.5 V or to a cut off capacity of 3.1 mAh/cm2. The calculated prelithiation degree ε of the anode was 21%.
While the disclosure has been described with reference to certain examples, those skilled in the art will appreciate that various modifications, changes, omissions, and substitutions can be made without departing from the spirit of the disclosure. It is intended, therefore, that the present disclosure be limited only by the scope of the following claims.
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/CN2016/085901 | 6/15/2016 | WO | 00 |
