Patent Application
20240291105
This invention relates to copolyester films and other articles made therefrom, and methods for their synthesis. In particular, the present invention is concerned with copolyester films which exhibit the properties required for use as a separator in metal-ion batteries, particularly lithium-ion batteries.
Lithium-ion batteries are widely used in the field of rechargeable batteries which is set to continually grow over the foreseeable future due, in part, to the increasing demand for consumer electronics and storage of renewable energy. During battery operation (i.e. during charging and discharging), lithium ions are transferred between the anode and cathode. Commercially available lithium-ion batteries are usually provided as wet-cell batteries which contain liquid or gel electrolytes containing lithium salts and a microporous separator. The microporous separator is placed between and in contact with two active solid electrodes. Generally, microporous separators for lithium-ion batteries have a thickness of about 20 μm to about 25 μm and are based on drawn polyolefin films (particularly polyethylene and polypropylene). The separator enables the movement of the liquid or gel electrolyte through its pores, thereby enabling movement of the lithium ions, but prevents direct electric contact between the anode and cathode in the battery. However, there remain concerns about the safety of wet-cell lithium-ion batteries, which have been known to catch fire or even explode. The porous network can lead to growth of lithium dendrites between the anode and cathode, which can result in short-circuiting of the battery, thermal run-away and flammability. The flammability risk is exacerbated by the relatively low glass transition and melting temperatures of these polyolefins. A further disadvantage of polyolefin films as separators is the relatively low mechanical strength, particularly the relatively low tensile strength in the transverse direction of a biaxially drawn film.
Dry-cell batteries have been developed which reduce some of the above safety concerns. These dry-cell batteries contain a solid separator between the cathode and anode, which prevents contact between the electrodes and provides a physical barrier to the growth of dendrites. In dry-cell batteries, the potentially flammable liquid electrolyte is eliminated. Thus, the separator must effectively function as both separator and electrolyte, and so for lithium-ion batteries the separator must enable migration of the lithium ions within its structure. Such lithium-conductive solid separators can be broadly categorised into two groups.
The first group focuses on the use of inorganic lithium-ion conductors based on ceramics such as LiPON (lithium phosphorous oxynitride, Li2PO2N), LLTO (lithium lanthanum titanium oxide) or LGPS (Li10GeP2S12). Typically, conductivities of up to 10−1 Scm−1 are attainable with ceramic separators. Such inorganic lithium-ion conductors are provided as thin films, which are commonly deposited using sputtering methods. However, deposition rates are low and processing has been limited to coin batteries which have small surfaces. Furthermore, during battery operation, the volume of the anodes and cathodes change and so the separator needs to accommodate these variations in volume. If the separator is too rigid, it may be damaged during the charging and discharging cycles or have limited cycling capability. This is a particular issue for ceramic separators, which are particularly rigid. The rigid and brittle nature of ceramic separators can also pose problems during separator manufacture, and during cell winding and assembly of batteries as the ceramic film is susceptible to cracking.
The second group focuses on the use of polymeric films comprising a polymeric matrix and a lithium salt such as LiClO4. WO2019/186173 discloses thin polymeric films comprising a copolyester which comprises repeating units derived from an aliphatic diol, an aromatic dicarboxylic acid and a poly(alkylene oxide), wherein the film further comprises lithium ions derived from lithium salts. Conductivities of such separators at room temperature are generally lower than ceramic conductors.
It is an object of the present invention to address one or more of the aforementioned problems. In particular, it is an object of the present invention to provide improved films for use as separators in a metal-ion solid state battery, i.e. the dry cell arrangement noted above, or in a metal-ion battery that comprises liquid or gel electrolytes. It is a particular object to provide improved films for use as separators in a metal-ion solid state battery. It is a particular object to provide films which at least maintain, and preferably improve, the conductivities of existing metal-conductive separators, whilst exhibiting good mechanical strength compared to ceramic separators, particularly reduced brittleness and/or improved flexibility. It is a particular object of the present invention to provide films which at least maintain and preferably improve the conductivities of existing metal-conductive separators, which exhibit good mechanical strength compared to ceramic separators, particularly reduced brittleness and/or improved flexibility, while ensuring ease of film formation and hence improving efficiency and economy of manufacture. It is a further object of the invention to provide such film separators which allow the thickness and/or weight thereof to be reduced while at least maintaining mechanical performance, so that the volume and/or weight of the battery can be reduced. Desirably, the film separators should exhibit flexibility without brittleness.
The present invention is particularly directed to lithium-ion batteries. Thus, the terms “metal ion”, “metal”, “metal-conductive separator” and “metal-ion battery” as used in the preceding paragraph and in the corresponding context hereinbelow preferably refer to “lithium ion”, “lithium”, “lithium-conductive separator” and “lithium-ion battery”, respectively. However, the present invention is also applicable to other rechargeable metal-ion batteries, including sodium, potassium, calcium, magnesium and aluminium, particularly sodium, magnesium and aluminium, and particularly sodium.
According to a first aspect, there is provided a copolyester film comprising a copolyester which comprises repeating units derived from a diol, a dicarboxylic acid and a poly(alkylene oxide), wherein the copolyester film further comprises a first metal ion-containing component selected from conductive ceramic particulate materials, and wherein the film may further comprise additional metal ions from one or more sources other than said conductive ceramic particulate material.
It will be appreciated that, for utility in a metal-ion battery, the metal of said first metal ion-containing component of said film is preferably the same as the metal of said additional metal ions (which is also referred to hereinbelow as the second metal ion-containing component).
Preferably, said first metal ion-containing component is a first lithium ion-containing component, and in that instance said additional metal ions are preferably additional lithium ions. Alternatively, said first metal ion-containing component is a first sodium ion-containing component, and in that instance said additional metal ions are preferably additional sodium ions.
Preferably, the copolyester film comprises said additional metal ions. Where present, said additional metal ions are preferably present in the form of a second metal ion-containing component, preferably selected from metal salts, preferably selected from lithium or sodium salts, preferably selected from lithium salts.
Thus, in a preferred embodiment, the first aspect of the present invention provides a copolyester film comprising said copolyester, a first metal ion-containing component selected from conductive ceramic particulate materials, and a second metal ion-containing component selected from metal salts. It will be appreciated that said first and second metal ion-containing components are different from each other.
In a particularly preferred embodiment, the first aspect of the present invention provides a copolyester film comprising said copolyester, a first lithium ion-containing component selected from conductive ceramic particulate materials, and a second lithium ion-containing component selected from lithium salts. It will be appreciated that said first and second lithium ion-containing components are different from each other.
In an alternative embodiment, the first aspect of the present invention provides a copolyester film comprising said copolyester, a first sodium ion-containing component selected from conductive ceramic particulate materials, and a second sodium ion-containing component selected from sodium salts. It will be appreciated that said first and second sodium ion-containing components are different from each other.
The copolyester films of the invention are suitable as separators, and particularly suitable as a solid electrolyte. Thus, the copolyester films exhibits volume conductivity rather than merely surface conductivity. The inventors have surprisingly found that the films of the present invention are suitable as solid separators which exhibit an excellent combination of good conductivity, high mechanical strength (particularly reduced brittleness and/or improved flexibility), while attaining such performance at relatively low thickness, and also while allowing efficient and reliable manufacture. Such separators exhibit excellent dimensional stability, particularly at elevated temperatures, and are able to tolerate the volume variations of electrodes during typical battery cycling.
As used herein, the term “copolyester” refers to a polymer which comprises ester linkages and which is derived from three or more types of comonomers. The copolyesters described herein are thermoplastic.
Suitable dicarboxylic acids for the copolyester include aromatic dicarboxylic acids such as terephthalic acid, isophthalic acid, phthalic acid and naphthalene dicarboxylic acid (such as 2,5-, 2,6- or 2,7-naphthalene dicarboxylic acid), as well as aliphatic dicarboxylic acids such as succinic acid, sebacic acid, adipic acid and azelaic acid. Cycloaliphatic dicarboxylic acids may also be used. Other suitable dicarboxylic acids include 4,4′-diphenyldicarboxylic acid and hexahydro-terephthalic acid. Preferably, the dicarboxylic acid used in the present invention is an aromatic dicarboxylic acid, preferably terephthalic acid or isophthalic acid, preferably terephthalic acid.
The copolyester preferably comprises at least one aromatic dicarboxylic acid, preferably terephthalic, isophthalic, or naphthalene dicarboxylic acids, and preferably terephthalic acid or isophthalic acid, and preferably terephthalic acid. In a first and most preferred embodiment, the dicarboxylic acid component comprises only one aromatic dicarboxylic acid. In a second embodiment, the dicarboxylic acid component comprises a first aromatic dicarboxylic acid (preferably terephthalic acid or isophthalic acid, preferably terephthalic acid) and a second dicarboxylic acid. The second dicarboxylic acid may be selected from aliphatic dicarboxylic acids such as succinic acid, sebacic acid, adipic acid or azelaic acid, and in one embodiment the second dicarboxylic acid is azelaic acid.
Suitable diols for the copolyester include acyclic, alicyclic and aromatic dihydroxy compounds. Preferred diols have 2-15 carbon atoms, and include ethylene, propylene, isobutylene, tetramethylene, 1,4-pentamethylene, 2,2-dimethyltrimethylene, hexamethylene and decamethylene glycols, dihydroxycyclohexane, cyclohexane dimethanol, resorcinol, hydroquinone, and 1,5-dihydroxynaphthalene, etc. An aliphatic diol is preferred, especially acyclic aliphatic diols containing 2-8 carbon atoms, especially aliphatic diols containing 2-4 carbon atoms. An unbranched aliphatic diol is preferred. Preferably the diol is selected from ethylene glycol, 1,3-propanediol and 1,4-butanediol, more preferably from ethylene glycol and 1,4-butanediol, and most preferably ethylene glycol. Cycloaliphatic (alicylic) glycols such as 1,4-cyclohexanedimethanol (CHDM) can also be used. Equivalent ester-forming derivatives of diols may be used in place of said diol. Preferably, the copolyester comprises only one type of diol residue. In one embodiment, at least 90 mol %, preferably at least 95 mol %, preferably at least 98 mol %, and preferably at least 99 mol % of said diol fraction is made up of one type of diol.
Suitable poly(alkylene oxide)s for the copolyester are preferably selected from C2 to C15, preferably C2 to C10, preferably C2 to C6 alkylene chains. The poly(alkylene oxide) may be selected from polyethylene glycol (PEG), polypropylene glycol (PPG) and poly(tetramethylene oxide) glycol (PTMO), preferably polyethylene glycol. Ethylene oxide-terminated poly(propylene oxide) segments may also be used. In one embodiment, the copolyester comprises only one type of poly(alkylene oxide) residue. In an alternative embodiment, the copolyester comprises two or more types of poly(alkylene oxide) residues, such as mixture of polyethylene glycol (PEG) and polypropylene glycol (PPG).
The number average molecular weight (MN) of the poly(alkylene oxide) glycol is preferably from about 200 g/mol to about 20000 g/mol, preferably from about 200 g/mol to about 6000 g/mol, preferably from about 200 g/mol to about 5000 g/mol, preferably no more than about 5000 g/mol, preferably no more than about 4000 g/mol, preferably from about 400 g/mol to about 3900 g/mol, preferably at least about 500 g/mol, preferably from about 500 g/mol to about 3800 g/mol, most preferably from about 500 g/mol to about 3700 g/mol, preferably from about 800 g/mol to about 3600 g/mol, preferably from about 1000 g/mol to about 3600 g/mol, preferably from about 2000 g/mol to about 3500 g/mol, and preferably from about 3350 to about 3450 g/mol, and preferably about 3350 g/mol or about 3450 g/mol. The number average molecular weight (MN) of the poly(alkylene oxide) is preferably at least about 200 g/mol, preferably at least about 400 g/mol, preferably at least about 500 g/mol, and preferably at least about 800 g/mol, for example at least about 1000 g/mol. The number average molecular weight (MN) of the poly(alkylene oxide) is preferably no more than about 20000 g/mol, preferably no more than about 5000 g/mol, preferably no more than about 4000 g/mol, and preferably no more than about 3800 g/mol, for example no more than about 3700 g/mol.
It has been found that if the molecular weight of the poly(alkylene oxide) is too high, it becomes harder to co-polymerise with the dicarboxylic acid and aliphatic diol to form a copolyester with a sufficiently high melt viscosity for reliable film formation, particularly in a melt extrusion process. In addition, it has been found that if the molecular weight of the poly(alkylene oxide) is too high, the conductivity may decrease.
Unless the context indicates otherwise the term molecular weight as used herein refers to number average molecular weight (MN) which is measured by the method as described herein.
The polydispersity index, PDI, (or dispersity, Ð) is defined as MW/MN. where MW is the weight average molecular weight. The polydispersity index is a measure of the uniformity (or heterogeneity) of the size of the different macromolecules that comprise a polymer (which is a mixture of macromolecules of different sizes). Compositions with a polydispersity index of 1 (i.e. which are monodisperse) consist of macromolecules each of which has the same size (such as dendrimers). Monodisperse compositions of macromolecules are typically made by non-polymerisation processes and are typically not referred to as polymers.
The poly(alkylene oxide) of the copolyester preferably has a polydispersity index of above 1, preferably at least about 1.01, preferably at least about 1.1, preferably at least about 1.2, and preferably no more than about 2.0, preferably no more than about 1.8, preferably no more than about 1.6, and preferably from about 1.01 to about 2.0, preferably about 1.1 to about 1.8, and preferably about 1.2 to about 1.6.
The copolyesters may be block (segmented) copolymers comprising alternating random-length sequences joined by ester linkages. Such copolyesters exhibit semi-crystalline (or hard) segments derived from an aromatic dicarboxylic acid and an aliphatic diol, and amorphous (or soft) segments derived from poly(alkylene oxide). Hard segments are made up of repeating units of [R1—O—C(═O)-A-C(═O)—O] wherein R1 is derived from the aliphatic diol and A is the aromatic ring (preferably phenyl or naphthyl) derived from the aromatic dicarboxylic acid defined hereinabove. Soft segments are made up of repeating units of [R—O] where R is the alkylene chain from the poly(alkylene oxide). The soft segments may be end-capped with said aromatic dicarboxylic acid via an ester linkage.
In a further embodiment, the copolyesters are random copolymers, in which the aromatic dicarboxylic acid, aliphatic diol and poly(alkylene oxide) units are arranged in a random sequence in the copolyester backbone.
Between these two extremes of random and block copolymers lie copolyesters which are referred to herein as “block-like” copolymers. In the block-like copolymers, the poly(alkylene oxide) units are interspersed between the aromatic dicarboxylic acid units to a greater degree than in the block copolymers, such that the crystalline (or hard) segments noted above are, on average, significantly shorter than in the block copolymers. The sequence of the comonomer units in the copolymer chain, i.e. the degree of randomness of the copolyester, may be determined using conventional techniques known in the art, and preferably by 13C NMR spectroscopy as described herein. The copolyester can be characterised as a block, block-like or random copolyester by quantifying the degree of randomness, B, with a value of 0 representing a pure block copolymer and a value of 1 representing a statistically random copolymer as defined by a Bernoulli model.
Preferably, B is in the range of from about 0.1 to 1.0, preferably from about 0.2 to about 0.95, preferably from about 0.3 to about 0.9, preferably from about 0.4 to about 0.8, for example from about 0.5 to about 0.7. The copolyester preferably has a value of B of at least about 0.1, preferably at least about 0.2, preferably at least about 0.3, and preferably at least about 0.4, for example at least about 0.5. The copolyester preferably has a value of B of no more than 1.0, preferably no more than about 0.95, preferably no more than about 0.9, preferably no more than about 0.8, and preferably no more than about 0.7.
Preferably, the copolymers of the present invention are the “block-like” copolyesters or the random copolyesters.
More preferably, the copolymers of the present invention are the “block-like” copolyesters, which are obtainable by selecting the molecular weight for the poly(alkylene oxide) as described herein.
It has been found that the molecular weight of the poly(alkylene oxide) has a significant influence on the sequence of the comonomers in the copolymer, and the characterisation of the copolymer as a block, block-like or random copolymer. Thus, lower molecular weight poly(alkylene oxide)s favour the formation of random copolymers, and higher molecular weight poly(alkylene oxide)s favour the formation of block copolymers. Block copolymers typically exhibit a greater tendency to crystallise and a higher melting temperature, relative to the corresponding random copolymers. Higher melting temperatures are preferably avoided in the present invention, since they require higher processing temperatures and there is a greater risk of degradation. In addition, it is preferred in the present invention to avoid the increased tendency of the pure block copolymers to crystallise, since this may hinder the migration of metal ions within the structure of the copolymer and may reduce its conductivity.
The poly(alkylene oxide) preferably constitutes from about 0.1 to about 80 wt %, preferably from about 5 to about 78 wt %, preferably from about 10 to about 75 wt %, preferably from about 12 to about 65 wt %, preferably from about 15 to about 60 wt %, preferably from about 16 to about 55 wt % by total weight of the copolyester.
Preferably, the poly(alkylene oxide) constitutes at least about 0.1 wt %, preferably at least about 5 wt %, preferably at least about 10 wt %, preferably at least about 12 wt %, preferably at least about 15 wt %, preferably at least about 16 wt %, preferably no more than about 80 wt %, preferably no more than about 78 wt %, preferably no more than about 75 wt %, preferably no more than about 65 wt %, preferably no more than about 60 wt %, preferably no more than about 55 wt % by total weight of the copolyester.
Where the copolyester comprises repeating units derived from a diol (preferably ethylene glycol), terephthalic acid and a poly(alkylene oxide), the poly(alkylene oxide) is preferably present in an amount of from about 5 to about 30 wt %, preferably from about 10 to about 25 wt %, preferably from about 15 to about 20 wt % of the total weight of the copolyester.
Where the copolyester comprises repeating units derived from a diol (preferably ethylene glycol), isophthalic acid and a poly(alkylene oxide), the poly(alkylene oxide) is preferably present in an amount of from about 35 to about 65 wt %, preferably from about 40 to about 60 wt %, preferably from about 45 to about 55 wt % of the total weight of the copolyester.
The amount of copolyester present in the copolyester film is preferably no more than about 99.9 wt % by total weight of the copolyester film, preferably no more than about 95 wt %, preferably no more than about 92 wt %, preferably no more than about 90 wt %. Preferably, the amount of copolyester present in the copolyester film is at least about 40% by total weight of the copolyester film, preferably at least about 50 wt %, preferably at least about 65 wt %, preferably at least about 80 wt %. Thus, the amount of copolyester present is preferably from about 40 wt % to about 99.9 wt %, preferably from about 50 wt % to about 95 wt %, preferably from about 65 wt % to about 92 wt %, preferably from about 80 to about 90 wt % by total weight of the copolyester film.
Said copolyester is preferably the only polyester present in the film.
The copolyester films of the present invention comprise a first metal-ion-containing component, which is selected from conductive ceramic particulate materials. Preferably, the copolyester films of the present invention comprise a first lithium ion-containing component, which is selected from conductive ceramic particulate materials. One or more conductive ceramic particulate materials may be present.
It will be appreciated by those skilled in the art that a ceramic material is an inorganic non-metallic solid comprising both metallic and non-metallic elements which is formed or densified by heating at high temperatures. Ceramic materials are typically hard, brittle and corrosion resistant, with low chemical reactivity and high melting points. The ceramic materials referred to herein may be crystalline or glassy. The ceramic particulate materials used in the present invention are conductive. The invention is primarily illustrated below in respect of lithium ion-containing conductive ceramic particulate materials, but the technical principles are generally applicable to other metal ion-containing conductive ceramic particulate materials.
Any suitable lithium ion-containing conductive ceramic particulate material may be used, particularly NASICON-type ceramic particulate materials (such as lithium ion-containing conductive glass ceramic particulate materials), LISICON-type ceramic particulate materials, perovskite-type oxide ceramic particulate materials, garnet-type oxide ceramic particulate materials, lithium phosphorus oxynitride (LIPON)-type ceramic particulate materials and lithium aluminium silicate (LAS) ceramic particulate materials.
As is known in the art, NASICON (sodium super ionic conductor) materials refer to a family of solids with the chemical formula Na1+xZr2SixP3−xO12 where 0<x<3, as well as analogous compounds where Na, Zr and/or Si are replaced by isovalent elements, and so in the context of the most preferred aspect of the present invention the sodium is replaced with lithium. Particularly suitable lithium-containing NASICON-type ceramic particulate materials may have the general formula LiMy(PO4)3, where M denotes a multivalent metal ion. For example, M may be selected from one or more of Al, Si, Ti, Zr, Ge, Sn and Hf. Other suitable lithium-containing NASICON-type ceramic particulate materials may have the general formula Li1+xMxTi2−x(PO4)3 (LATP), where M denotes a trivalent cation selected from one or more of Al, Sc, Y and La. Other suitable lithium-containing NASICON-type ceramic particulate materials may have the general formula Li1+xAlxGe2−x(PO4)3 (LAGP), for example wherein x is 0.5.
Particularly suitable are lithium ion-containing conducting glass ceramic particulate materials which have a NASICON-structure. Preferred particulate materials are those commercially available under the tradename “LICGC” from Ohara Inc. A preferred particulate material is commercially available as LICGC™ PW-01 powder from Ohara Inc., which is understood as having a main crystalline phase of Li1+x+yAlxTi2−xSiyP3−yO12 and a composition of Li2O—Al2O3—SiO2—P2O5—TiO2. A further preferred particulate material is commercially available as LICGC™ AG-01 from Ohara Inc., which is understood as having a main crystalline phase of Li1+x+yAlx(Ti,Ge)2−xSiyP3−yO12 and a composition of Li2O—Al2O3—SiO2—P2O5—TiO2—GeO2.
As is known in the art, LISICON (lithium super ionic conductor) materials refer to a family of solids with the chemical formula Li2+2xZn1−xGeO4. As with NASICON-type materials, other elements (typically isovalent elements) may replace the Li, Zn and/or Ge. Suitable LISICON-type particulate materials may be selected from Li2+2xZn1−xGe4O16, Li14ZnGe4O16, Li(3+x)GexV(1−x)O4, Li(4−x)Si(1−x)PxO4, and thio-LISICONs such as those having the formula Li(4−x)Ge(1−x)PxS4 Li10GeP2S12, where x is between 0 and 1.
Suitable perovskite-type oxide particulate materials may be selected from Li3xLa(2/3)−xTiO3 (LLTO) and Li3xLa1/3−xTaO3.
Suitable garnet-type oxide particulate materials may have the general formula Li7−3y−xLa3Zr2−xM1yM2xO12 (where M1 denotes a trivalent cation such as Al and Ga, M2 denotes a pentavalent cation such as Nb and Ta, x≥0 and y≤2); Li5La3M2O12 (where M denotes Nb and/or Ta); Li6ALa2M2O12 (where A denotes Ca, Sr and/or Ba, and M denotes Nb or Ta); or Li6.5La2.5Ba0.5ZrTaO12.
Suitable LIPON-type ceramic particulate materials may have the general formula LixPOyNz, such as Li2PO2N.
Suitable LAS ceramic particulate materials may be selected from AlLiO6Si2.
With regard to sodium ion-containing ceramic particulate materials, particularly suitable are NASICON-type ceramic particulate materials (such as sodium ion-containing conductive glass ceramic particulate materials), beta-alumina and beta”-alumina phases Na2O·nAl2O3 where 5≤n≤11, sodium rare earth silicates, and Na-ion conducting oxyhalide glasses. Suitable NASICON-type ceramic particulate materials are NASICON-structured oxides, which may have the general formula Na3Zr2Si2PO12, NaTi2(PO4)3, NaGe2(PO4)3 or Na1+x[SnxGe2−x(PO4)3]. Suitable sodium rare earth silicates have the general formula Na5MSi4O12, where M is Y, Sc, Lu and/or any trivalent rare earth cation. Suitable Na-ion conducting oxyhalide glass may be NaI—NaCl—Na2O—B2O3.
Preferably, the volume distributed median particle diameter (equivalent spherical diameter corresponding to 50% of the volume of all the particles, read on the cumulative distribution curve relating volume % to the diameter of the particles—often referred to as the “Dv50” or “D50” value) of the conductive ceramic particulate material is in the range from 0.01 to 5 m, preferably from 0.05 to 3 m, preferably from 0.1 to 2 m, preferably from 0.2 to 1.5 m, preferably from 0.4 to 1.0 m. The particle size may be measured by laser light diffraction (preferably Fraunhofer diffraction). A particularly preferred method utilises a Mastersizer (e.g. a 3000) available from Malvern. The median particle size may be determined by plotting a cumulative distribution curve representing the percentage of particle volume below chosen particle sizes and measuring the 50th percentile.
The amount of said metal ion-containing conductive ceramic particulate material present in the copolyester film is preferably no more than about 60 wt % by total weight of the copolyester film, preferably no more than about 50 wt %, preferably no more than about 35 wt %, preferably no more than about 20 wt %, and preferably at least about 0.1 wt %, preferably at least about 5 wt %, preferably at least about 8 wt %, preferably at least about 10 wt %. Thus, the amount of conductive ceramic particulate material present is preferably from about 0.1 wt % to about 60 wt %, preferably from about 5 wt % to about 50 wt %, preferably from about 8 wt % to about 35 wt %, preferably from about 10 to about 20 wt % by total weight of the copolyester film.
Said metal ion-containing conductive ceramic particulate material is held within the polymeric matrix of the film.
As described hereinabove, the copolyester films of the present invention preferably comprise additional metal ions from one or more sources other than said conductive ceramic particulate material. Where the conductive ceramic particulate material is a lithium-ion containing conductive ceramic particulate material, the copolyester film preferably comprises additional lithium ions from one or more sources other than said conductive ceramic particulate material. Where the conductive ceramic particulate material is a sodium-ion containing conductive ceramic particulate material, the copolyester film preferably comprises additional sodium ions from one or more sources other than said conductive ceramic particulate material. These additional metal ions are referred to herein as the second metal ion component, for instance as the second lithium ion component or the second sodium ion component. It will be appreciated that said first metal ion-containing component and said second metal ion component are different from each other. The second metal ion component is preferably a metal ion-containing component selected from metal salts. The invention is primarily illustrated below in respect of lithium salts, but the technical principles are generally applicable to other metal salts materials.
Any suitable lithium salt may be used. One or more different types of lithium salts may be used. Preferably the lithium salts are selected from lithium salts suitable for use in lithium ion batteries, such as lithium bis(trifluoromethanesulfonyl)imide (LiTFSI), lithium hexafluorophosphate (LiPF6), lithium tetrafluoroborate (LiBF4), lithium thiocyanate (LiSCN), lithium hexafluoroarsenate (LiAsF6), lithium trifluoromethanesulfonate (LiCF3SO3), lithium bromide (LiBr), lithium iodide (LiI), lithium bis(trifluoromethanesulfonimide) (LiN(CF3SO2)2), lithium tris(trifluoromethylsulfonyl)methide (LiC(CF3SO2), lithium orthosilicate, lithium trifluoroacetate (LiCF3CO2) and lithium bis(fluorosulfite)amide (LiN(FO2S)2).
When the copolyester film is formed using solvent casting techniques, it is preferred that the metal ion is derived from a metal salt which has high solubility in the solvent used in the solvent re-casting steps. Thus, in the case of lithium ion batteries, a particularly preferred lithium salt is lithium trifluoromethanesulfonate (LiCF3SO3).
The metal salts (including the preferred lithium salts) may be selected from:
Optionally, the metal salts are selected from metal salts of (i) to (v) provided above.
Thus, suitable lithium salts include: dilithium terephthalate (DLTA), dilithium isophthalate, lithium glycolate, lithium benzoate, lithium acetate, lithium carbonate, lithium perchlorate, lithium orthosilicate, lithium phosphate, lithium salicylate, lithium succinate and lithium bis(oxalato)borate.
Preferably the metal salt is an organic metal salt.
In a preferred embodiment, the metal salt is the salt of the aromatic dicarboxylic acid from which the copolyester is derived. Thus, in the case of the preferred copolyesters derived from terephthalic acid, the lithium salt is preferably selected from mono- or di-lithium terephthalate, and preferably dilithium terephthalate. The inventors have found that dilithium terephthalate is particularly preferable for thermal stability and cost reasons. In the case of the preferred copolyesters derived from isophthalic acid, the lithium salt is preferably selected from mono- or di-lithium isophthalate, and preferably dilithium isophthalate.
Other preferred metal salts may be selected from the alkoxylate esters of the aforementioned acids, particularly the carboxylic acids, particularly the dicarboxylic acids, particularly the aromatic dicarboxylic acids, particularly terephthalic acid. Such alkoxylate esters are preferably derived from the aliphatic diols, preferably from C2-10 aliphatic diols, preferably from C2-6 aliphatic diols, preferably from C2, C3 or C4 aliphatic diols, more preferably from ethylene glycol, 1,3-propanediol and 1,4-butanediol, more preferably from ethylene glycol.
A particularly suitable lithium salt has the formula (I) below, and is referred to herein as dilithium bis hydroxy ethyl terephthalate (DL-BHET):
Preferably the lithium salt is selected from lithium trifluoromethanesulfonate (LiCF3SO3), dilithium terephthalate or dilithium bis hydroxy ethyl terephthalate. Preferably the lithium salt is selected from dilithium terephthalate.
With regard to the sodium-containing embodiment of the present invention, any suitable sodium salt may be used. One or more different types of sodium salts may be used. It will be appreciated that the preferences and elements described in respect of the lithium salt apply equally to the sodium salt, except that the lithium ions are replaced by sodium ions. Preferably, the sodium salt is selected from sodium nitrate (NaNO3), sodium perchlorate (NaClO4), sodium tetrafluoroborate (NaBF4), sodium hexafluorophosphate (NaPF6), sodium bis(trifluoromethanesulfonyl)imide (NaTFSI), sodium bis(trifluoromethane)sulfonimide (Na[N(CF3SO2)2]), sodium hexafluoroarsenate(V) (NaAsF6), sodium bis(oxalatoborate) (“NaBOB”), sodium halides (NaX), where X=Cl, Br or I, sodium thiocyanate (NaSCN), sodium pentacyanopropenide (NaPCPI), sodium tetracyanopirolate (NaTCP) and sodium tricyanoimidazolate (NaTIM).
In one embodiment, the metal ions of said second metal ion component are present in and held within the polymeric matrix of the film by virtue of the interaction between the metal cations and the polarisable electronegative oxygen atoms of the copolyester, preferably at least the electronegative oxygen atoms of the polyalkylene oxide units.
In a preferred embodiment, the metal ions of said second metal ion component are held within the polymeric matrix of the film by virtue of the interaction between the metal cations and the anion of a metal salt. Thus, in this embodiment, the copolyester film comprises a metal salt. Preferably at least part, preferably at least 50 wt %, preferably at least 60 wt %, preferably at least 70 wt %, preferably at least 80 wt %, preferably at least 90 wt %, preferably at least 95 wt %, preferably at least 99 wt %, and preferably substantially all of the metal ions of said second metal ion component are in the form of a metal salt. The metal salt is preferably the metal salt from which the metal ions are derived. The metal salts are selected from the metal salts described above, and the preferences described above apply here. Thus, in this preferred embodiment, a metal salt is held within the polymeric matrix. In this embodiment, the metal salt is not part of the polymer backbone, i.e. it has not been polymerised into the copolyester. In other words, in this preferred embodiment, the anion of the metal salt is not covalently bound to the copolyester. In the preferred embodiment described above in which the metal salt is the salt of the same aromatic dicarboxylic acid from which the copolyester is derived, the metal-containing copolyester film described herein exhibits excellent thermal stability which is believed to result from the alignment of the morphology of the copolyester with the morphology of the metal salt.
The amount of metal ions of said second metal ion component in the copolyester film is preferably effective to provide a metal:O molar ratio of from about 5:1 to about 1:50, preferably from about 4:1 to about 1:50, preferably from about 3:1 to about 1:50, preferably from about 2:1 to about 1:50, preferably about 1:1 to about 1:40, preferably about 1:2 to about 1:30, preferably about 1:4 to about 1:25, wherein the number of O atoms in this ratio is defined as the number of 0 atoms in the poly(alkylene oxide) residues, and the number of metal atoms in this ratio is defined as the number of metal atoms provided by said additional metal ions (i.e. said second metal ion component, and excluding said first metal ion-containing component).
Preferably, the amount of the second metal ion component (i.e. preferably said metal salts) is no more than about 40 wt %, preferably no more than about 10 wt %, and preferably at least about 0.1%, preferably at least about 1%, and preferably from about 0.1 wt % to about 40 wt %, preferably from about 1 wt % to about 10 wt % by total weight of the copolyester film.
Where the copolyester films of the present invention comprise said second metal ion component, the total amount of the first metal ion-containing component and the second metal ion component is preferably no more than about 60 wt % by total weight of the copolyester film, preferably no more than about 50 wt %, preferably no more than about 35 wt %, preferably no more than about 20 wt %, and preferably at least about 0.1 wt %, preferably at least about 5 wt %, preferably at least about 8 wt %, preferably at least about 10 wt %. Thus, the total amount of the first metal ion-containing component and the second metal ion component present is preferably from about 0.1 wt % to about 60 wt %, preferably from about 5 wt % to about 50 wt %, preferably from about 8 wt % to about 35 wt %, preferably from about 10 to about 20 wt % by total weight of the copolyester film.
The copolyester, first metal ion-containing component and, where present, the second metal ion component are the major component of the film, and preferably make up at least about 65%, preferably at least about 75%, preferably at least about 85%, preferably at least about 95%, and preferably at least about 98% by weight of the total weight of the film.
The copolyester film of the present invention may further comprise any other additive conventionally employed in the manufacture of polyester films. Thus, agents such as anti-oxidants, UV-absorbers, hydrolysis stabilisers, cross-linking agents, dyes, fillers, pigments, voiding agents, lubricants, radical scavengers, thermal stabilisers, flame retardants and inhibitors, anti-blocking agents, surface active agents, slip aids, gloss improvers, prodegradents, viscosity modifiers and dispersion stabilisers may be incorporated as appropriate. Such additives may be introduced into the copolyester composition in a conventional manner. For example, the additive(s) may be introduced by mixing with the monomeric reactants from which the film-forming copolyester composition is derived, or the additive(s) may be mixed with the copolyester composition by tumble or dry blending or by compounding in an extruder, followed by cooling and, usually, comminution into granules or chips. Masterbatching technology may also be employed.
In a preferred embodiment, the film comprises an anti-oxidant. A range of antioxidants may be used, such as antioxidants which function by trapping radicals or by decomposing peroxide. Suitable radical-trapping antioxidants include hindered phenols, secondary aromatic amines and hindered amines, such as Tinuvin™ 770 (Ciba-Geigy). Suitable peroxide-decomposing antioxidants include trivalent phosphorous compounds, such as phosphonites, phosphites (e.g. triphenyl phosphate and trialkylphosphites) and thiosynergists (e.g. esters of thiodipropionic acid, such as dilauryl thiodipropionate). Hindered phenol antioxidants are preferred. A particularly preferred hindered phenol is tetrakis-(methylene 3-(4′-hydroxy-3′,5′-di-t-butylphenyl propionate) methane, which is commercially available as Irganox™ 1010 (Ciba-Geigy). Other suitable commercially available hindered phenols include Irganox™ 1035, 1076, 1098 and 1330 (Ciba-Geigy), Santanox™ R (Monsanto), Cyanox™ antioxidants (American Cyanamid) and Goodrite™ antioxidants (BF Goodrich). The concentration of antioxidant present in the film is preferably in the range from 50 ppm to 5000 ppm, more preferably in the range from 300 ppm to 1500 ppm, particularly in the range from 400 ppm to 1200 ppm, and especially in the range from 450 ppm to 600 ppm based on the weight of the copolyester. A mixture of more than one antioxidant may be used, in which case the total concentration thereof is preferably within the aforementioned ranges. Incorporation of the antioxidant into the copolyester may be effected by conventional techniques, and preferably by mixing with the monomeric reactants from which the copolyester is derived, particularly at the end of the direct esterification or ester exchange reaction, prior to polycondensation.
In a further preferred embodiment, the film comprises an inorganic particulate filler, preferably selected from metalloid oxides (such as alumina, titania, zirconia, zinc oxide, talc and silica), calcined china clay, alkaline metal salts (such as the carbonates and sulphates of calcium and barium) and non-conductive ceramic particulate materials. The inorganic particulate filler should have a particle size which is smaller than the film thickness, and preferably the particle size is no more than 10 μm, preferably no more than about 5 μm, preferably no more than about 2 μm, preferably in the range of from about 0.5 μm to about 2.0 μm. It will be appreciated that the identity of said inorganic particulate filler (or indeed any other of said conventional additives) is a different entity from the first or second metal ion-containing components described hereinabove. In particular, said inorganic particulate filler (or any other of said conventional additives) does not contain the metal ion of the first or second metal ion-containing components described hereinabove, and hence said inorganic particulate fillers are referred to herein as “passive fillers” because they are not capable of direct transport of said metal ion. Nevertheless, such passive fillers have been found surprisingly to enhance the ionic conductivity generated by said first or second metal ion-containing components.
Thus, in a preferred embodiment of the first aspect of the invention, there is provided a copolyester film comprising a copolyester which comprises repeating units derived from a diol, a dicarboxylic acid and a poly(alkylene oxide), wherein the copolyester film further comprises a first metal ion-containing component selected from conductive ceramic particulate materials, wherein the copolyester film further comprises a passive filler.
And in a further preferred embodiment of the first aspect of the invention, there is provided a copolyester film comprising a copolyester which comprises repeating units derived from a diol, a dicarboxylic acid and a poly(alkylene oxide), wherein the copolyester film further comprises a first metal ion-containing component selected from conductive ceramic particulate materials, wherein the copolyester film further comprises a passive filler, and wherein the film further comprise additional metal ions from one or more sources other than said conductive ceramic particulate material and other than said passive filler.
Inorganic particulate fillers have routinely been added into polyester films in order to improve handling and windability during manufacture and downstream processing, and for such purposes the fillers are typically used in relatively minor amounts, generally such that the total weight of filler is not more than about 2.5%, preferably not more than about 2.0%, preferably not more than about 1.0%, more typically no more than about 0.6% and preferably no more than about 0.3% by weight, based on the total weight of the copolyester film. However, in the present invention, the passive filler is preferably used in amounts of at least 5 wt %, preferably at least about 7 wt %, preferably at least about 10 wt %, and preferably from about 5 wt % to about 20 wt %, preferably from about 7 wt % to about 20 wt %, preferably from about 7 wt % to about 15 wt %, by total weight of the copolyester film.
Where the film is formed via melt extrusion, the melt viscosity of the metal ion-containing copolyester from which the film is derived is preferably at least about 100 Pa·s, preferably not more than about 1000 Pa·s, preferably not more than about 500 Pa·s, preferably not more than about 300 Pa·s, preferably not more than about 250 Pa·s, and preferably about 150 Pa·s, at the desired processing temperature. Typical processing temperatures at which the copolyester should exhibit such melt viscosities are those used in the manufacture of the film described herein, and are preferably in the range of 200 to 290° C., particularly 220 to 280° C., and preferably at 275° C., and/or wherein the copolyester exhibits such melt viscosities at a temperature within the range of TM to TM+10° C. wherein TM is the crystalline melting temperature of the copolyester. A melt viscosity which is too high can lead to difficulties in film manufacture and/or reduce the molecular weight of the final copolyester and/or increase the cost of film manufacture, for instance because of the need to utilise specialised film-forming equipment. In addition, a melt viscosity which is too high may require a reduction in the output rate of the extruder, thereby decreasing the efficiency and economy of manufacture, or require an increase to the extrusion temperature in order to reduce the viscosity of the melt (which in turn can lead to thermal degradation of the polymer and the loss of associated properties), in order to achieve stable film production. A melt viscosity which is too low can lead to difficulties in reliable film formation and stretching.
The copolyester films described herein are preferably oriented copolyester films, preferably biaxially oriented copolyester films.
The copolyester films described herein are preferably self-supporting films, i.e. they are capable of independent existence in the absence of a supporting base.
The thickness of the film is preferably at least about 5 μm, preferably at least about 10 μm, preferably at least about 15 μm, and preferably at least about 20 μm. The thickness of the film is preferably no more than about 200 μm, preferably no more than about 150 μm, preferably no more than about 100 μm, preferably no more than about 85 μm, preferably no more than about 70 μm, preferably no more than about 50 μm, and preferably no more than about 35 μm. Thus, the thickness of the film is preferably from about 5 μm to about 200 μm, preferably from about 5 μm to about 150 μm, preferably from about 10 μm to about 100 μm, preferably from about 10 μm to about 85 μm, preferably from about 15 μm to about 70 μm, preferably from about 15 μm to about 50 μm and preferably from about 20 μm to about 35 μm.
Preferably the through-film ionic conductivity of the film is at least about 10−7 S/cm, preferably at least about 10−6 S/cm measured at 25° C.
Preferably the through-film ionic conductivity of the film is at least about 10−7 S/cm, preferably at least about 10−6 S/cm, preferably at least about 10−5 S/cm measured at 60° C.
The film should have low shrinkage, preferably less than 20%, preferably less than 15%, preferably less than 10% after 30 mins at 100° C. Preferably low shrinkage values are exhibited in both (orthogonal) dimensions of the film (i.e. the machine and transverse dimensions).
Preferably the crystalline melting point (Tm) of the film is greater than 175° C., preferably greater than 200° C., preferably greater than 210° C., preferably greater than 220° C., and these temperatures are particularly preferred for a PET-based copolyester. In comparison, polyolefin films conventionally used as microporous separators for lithium-ion, batteries typically have a crystalline melting point (Tm) of about 130° C. to 150° C. This relative increase in Tm is advantageous as the films described herein are therefore suitable for applications which require higher operating temperatures. Preferably the crystalline melting point (Tm) of the film is not more than 270° C.
Preferably, the film of the present invention exhibits a glass transition temperature (Tg) of no more than about 50° C., preferably no more than about 45° C., preferably no more than about 40° C. In the present invention, a lower Tg is preferred since it promotes greater conductivity at the operating temperature of the film in the preferred end-use described herein. The films of the present invention typically exhibit a Tg of at least about −50° C., preferably of at least about −30° C. and preferably of at least about −10° C.
The films described herein are particularly suitable as solid separators in a metal-ion rechargeable battery, particularly a dry-cell battery, also referred to herein as a solid-state battery.
According to a second aspect of the invention, there is provided a method of manufacturing a polyester film as defined in the first aspect herein, wherein said method comprises the steps of:
The copolyesters described herein can be synthesised according to conventional techniques for the manufacture of polyester materials. Thus, the copolyester may be made by a first step of direct esterification or trans-esterification, followed by a second step of polycondensation. In the direct esterification embodiment, the diol and dicarboxylic acid are reacted directly, typically under elevated temperature (typically about 150 to 260° C.) and pressure (typically about 40 psi) in the presence of a base (e.g. sodium hydroxide), and with the water by-product of the direct esterification reaction being distilled off, to form a bis(hydroxyalkyl)carboxylate. Once the direct esterification reaction is complete, a stabiliser (e.g. phosphoric acid) is added to neutralise the base. In an alternative embodiment, the copolyester is prepared by the trans-esterification route, which preferably comprises heating an ester of the dicarboxylic acid (suitably a lower alkyl (C1-4) ester, preferably the dimethyl ester) with a molar excess of the diol at elevated temperature (typically in the range of about 150 to 260° C.) in the presence of a basic esterification catalyst (e.g. manganese (II) acetate tetrahydrate, Mn(OAc)2·4H2O), and with the methanol by-product of the trans-esterification reaction being distilled off, to form a bis(hydroxyalkyl)carboxylate. Polymerisation is effected in a polycondensation step which is conducted using an appropriate catalyst, usually antimony trioxide, at elevated temperature (typically about 290° C.) and typically under reduced pressure (for instance about 1 mm Hg), with continuous distillation of by-product(s). The poly(alkylene oxide) may be present at the start of the synthetic procedure, since the dicarboxylic acid or dicarboxylic acid ester starting material typically reacts selectively with the diol rather than the poly(alkylene oxide), particularly as the molecular weight of the poly(alkylene oxide) increases. Preferably, however, the poly(alkylene oxide) is added at the start of the polycondensation step.
Preferably, the synthetic procedure further comprises a solid phase polymerisation (SSP) step to increase the molecular weight of the copolyester and increase and/or complete the polymerisation of the poly(alkylene oxide) into the copolyester.
Thus, the product of the polycondensation reaction (step (ii)) is preferably subjected to an SSP step. The solid phase polymerisation may be carried out in a fluidised bed, e.g. fluidised with nitrogen, or in a vacuum fluidised bed, using a rotary vacuum drier. Suitable solid phase polymerisation techniques are disclosed in, for example, EP-A-0419400 the disclosure of which is incorporated herein by reference. Thus, SSP is typically conducted at a temperature which is 10-50° C. below the crystalline melting point (TM) of the polymer but higher than the glass transition temperature (Tg) (or where the copolyester exhibits multiple glass transition temperatures, higher than the highest glass transition temperature). An inert atmosphere of dry nitrogen or a vacuum is used to prevent degradation. In a preferred embodiment, solid phase polymerisation is carried out over 16 hours at 220° C. under vacuum.
The first metal ion-containing component and optional second metal ion-containing component may be introduced into the copolyester independently or together. When introduced independently, the first metal ion-containing component and second metal ion-containing component may be introduced simultaneously or sequentially. Where either or both of the first and second metal ion-containing component(s) contain a plurality of different compounds, said plurality of compounds may be introduced into the copolyester independently or together, and when introduced independently they may be introduced simultaneously or sequentially.
In one embodiment, referred to herein as Embodiment A1, the first and second metal ion-containing components are introduced into the copolyester during synthesis of the copolyester in steps (i) and/or (ii). Preferably, the first and second metal ion-containing components are added to one or more of the reactant(s) or reaction mixture at the start of the synthetic procedure. Alternatively, the first and second metal ion-containing components are added to the reaction product of the direct esterification or trans-esterification step (i), and before the polymerisation stage (ii).
In a second embodiment, referred to herein as Embodiment A2, the first and second metal ion-containing components are introduced into the copolyester during a separate compounding or mixing step.
In a third embodiment, referred to herein as Embodiment A3, the first and second metal ion-containing components are introduced into the copolyester during different steps. For instance, the second metal ion-containing component is introduced during synthesis of the copolyester in steps (i) and/or (ii) (and preferably added to one or more of the reactant(s) or reaction mixture at the start of the synthetic) and the first metal ion-containing component is introduced during a separate compounding or mixing step.
Formation of the film may be effected by conventional melt-extrusion techniques well-known in the art. In general terms the process comprises the steps of extruding a layer of polymer at a temperature within a range appropriate to the melting temperature thereof, for instance in a range of from about 250 to about 300° C. (or, typically, no more than about 10° C. higher than the crystalline melting point of the polymer), quenching the extrudate and preferably orienting the quenched extrudate.
Orientation may be effected by any process known in the art for producing an oriented film, for example a tubular or flat film process. Biaxial orientation is effected by drawing in two mutually perpendicular directions in the plane of the film to achieve a satisfactory combination of mechanical and physical properties. Biaxial orientation may be effected by simultaneous orientation or by sequential orientation. Preferably simultaneous orientation is effected.
Simultaneous biaxial orientation may be effected, for instance, in a tubular process by extruding a thermoplastics polyester tube which is subsequently quenched, reheated and then expanded by internal gas pressure to induce transverse orientation, and withdrawn at a rate which will induce longitudinal orientation. Particularly suitable simultaneous biaxial orientation processes are disclosed in EP-2108673-A and US-2009/0117362-A1, the disclosure of which processes is incorporated herein by reference.
Another preferred technique is a flat film process in which the film-forming polyester is extruded through a slot die and rapidly quenched upon a chilled casting drum to ensure that the polyester is quenched to the amorphous state. Orientation is then effected by stretching the quenched extrudate in at least one direction at a temperature above the glass transition temperature(s) of the polyester. Sequential orientation may be effected by stretching a flat, quenched extrudate firstly in one direction, usually the longitudinal direction, i.e. the forward direction through the film stretching machine, and then in the transverse direction. Forward stretching of the extrudate is conveniently effected over a set of rotating rolls or between two pairs of nip rolls, transverse stretching then being effected in a stenter apparatus.
Stretching is generally effected so that the dimension of the oriented film is from 2 to 7, preferably from 2 to 5, more preferably 2.5 to 4.5, more preferably 3.0 to 4.5, more preferably 3.5 to 4.5 times its original dimension in the or each direction of stretching. Stretching is conventionally effected at temperatures higher than the Tg of the copolyester composition, preferably at least about 5° C. higher, preferably at least about 15° C. higher than the Tg, and preferably in the range of from about Tg+5° C. to about Tg+75° C., preferably from about Tg+5° C. to about Tg+30° C. Typically, stretching is effected at temperatures in the range of about 5 to about 155° C., preferably about 5 to about 110° C. Greater draw ratios (for example, up to about 8 times) may be used if orientation in only one direction is required. It is not necessary to stretch equally in the machine and transverse directions although this is preferred if balanced properties are desired.
Preferably, a simultaneous biaxial stretching process is used, which is particularly advantageous for making the thin films of the present invention.
A stretched film may be, and preferably is, dimensionally stabilised by heat-setting under dimensional support at a temperature above the glass transition temperature(s) of the copolyester but below the melting temperature (TM) thereof, to induce the desired crystallinity of the copolyester. During the heat-setting, a small amount of dimensional relaxation may be performed in the transverse direction (TD) and/or machine direction (MD). The dimensional relaxation of up to 10%, more typically up to about 8%. Dimensional relaxation in the transverse direction is referred to in the art as “toe-in”, and typically involves a dimensional shrinkage of up to about 5%, typically from about 2 to about 4%. Dimensional relaxation in the machine direction may be effected by conventional techniques, although it is a relatively more difficult process to achieve since low line tensions are required particularly in a sequential orientation process. For this reason, a simultaneous orientation process is preferably used where MD relaxation is desired and, in this embodiment, simultaneous relaxation in the MD and TD is typically effected. The actual heat-set temperature and time will vary depending on the composition of the film and its desired final thermal shrinkage but should not be selected so as to substantially degrade the toughness properties of the film such as tear resistance. Within these constraints, preferred films are heat-set at a temperature from about 80° C. less than the melting temperature of the film (i.e. TM−80° C.) to about 10° C. less than TM (i.e. TM−10° C.), preferably from about TM−70° C. to about TM−20° C. Thus, the heat-set temperature is suitably in the range of from about 130 to about 245° C., preferably from about 150 to about 245° C., and preferably at least 180° C., preferably in the range of 190 to 230° C. After heat-setting the film is typically quenched rapidly in order induce the desired crystallinity of the copolyester.
The film may be further stabilized through use of an in-line relaxation stage, particularly where the film has been oriented in a sequential orientation process. Alternatively the relaxation treatment can be performed off-line. The relaxation of the film is between 0% and 10%, preferably 5%. In this additional step, the film is heated at a temperature lower than that of the heat-setting stage, and with a much reduced MD and TD tension. For a relaxation process which controls the film speed, the reduction in film speed (and therefore the strain relaxation) is typically in the range 0 to 2.5%, preferably 0.5 to 2.0%. There is no increase in the transverse dimension of the film during the heat-stabilisation step. The temperature to be used for the heat stabilisation step can vary depending on the desired combination of properties from the final film, with a higher temperature giving better, i.e. lower, residual shrinkage properties. A temperature of 135 to 250° C. is generally desirable, preferably 150 to 230° C., more preferably 170 to 200° C. The duration of heating will depend on the temperature used but is typically in the range of 10 to 40 seconds, with a duration of 20 to 30 seconds being preferred. This heat stabilisation process can be carried out by a variety of methods, including flat and vertical configurations and either “off-line” as a separate process step or “in-line” as a continuation of the film manufacturing process. Film thus processed will exhibit a smaller thermal shrinkage than that produced in the absence of such post heat-setting relaxation.
Advantageously, the film may be and preferably is manufactured in air, i.e. wherein the film is not manufactured (including the steps of extrusion, casting and stretching) under the atmosphere of an inert gas (such as nitrogen or a noble gas such as argon). Thus, the copolyester compositions and films described herein are surprisingly thermally stable, and do not require any special handling conditions, in particular an inert atmosphere, during manufacture or storage.
As an alternative to forming the film by melt-extrusion, the copolyester film may be formed by conventional solvent casting techniques well-known in the art. In general terms, the process comprises forming a film from a dispersion comprising said copolyester, said first metal ion-containing component, said optional second metal ion-containing component and a solvent. Suitable solvents include N-methyl-2-pyrrolidone (NMP), acetonitrile (ACN), tetrahydrofuran (THF), dimethylformamide (DMF), dimethyl sulfoxide (DMSO), dimethyl carbonate (DMC), ethylene carbonate (EC), propylene carbonate (PC), dimethoxyethane (DME), methyl formate ((MF), nitromethane (NM), diethyl carbonate (DEC), toluene, water, ethanol, acetone, isopropyl alcohol, methanol, ethyal alcohol and ethyal acetate.
The type of mixing vessel, duration of the dispersion step and temperature of the dispersion step will vary depending on the type of copolyester and solvent used. Typically, the temperature used is between about 22° C. and about 100° C. Typically, the duration of the dispersion step will be several hours, for example between about 6 hours and 48 hours, between about 10 hours and 30 hours, between about 12 hours and 24 hours.
The first metal ion-containing component and optional second metal ion-containing component may already be present in the copolyester which is contacted with the solvent to form said dispersion. Alternatively, the first and second metal ion-containing components may be mixed with the copolyester dispersion, and in this embodiment said first and second metal ion-containing components may be introduced to said dispersion independently or together. When introduced independently, the first and second metal ion-containing components may be introduced simultaneously or sequentially. Where either or both of the first and second metal ion-containing components contain a plurality of different compounds, said plurality of compounds may be introduced independently or together, and when introduced independently they may be introduced simultaneously or sequentially.
The dispersion is then cast into a film on a support base. The cast film is then suitably dried in order to remove residual solvent. Typically, the cast film is dried at a temperature of from about 50° C. to about 170° C., preferably from about 80° C. to 160° C. It will be appreciated that the drying step may comprise multiple (e.g. at least two) drying steps across different temperature zones in order to reduce the amount of residual solvent. Once dried, the cast copolyester film may be removed from the support base for subsequent processing, for instance by incorporating into the battery, for instance as a separator.
If desired, a film prepared by solvent casting may also be subjected to orientation and dimensional stabilisation, as described hereinabove.
In other methods of film manufacture, the film-forming copolyester composition is cast onto a support base which itself is a component of the battery and in particular an electrode, i.e. the cast film is formed in situ during battery manufacture. This method of manufacture is of particular utility in the solvent-casting method, but is not limited thereto and may also be used for an extrusion method of film formation. Thus, in this embodiment, the separator of the battery is formed in situ by casting the copolyester film onto an electrode during battery manufacture. In that case, the composite structure of electrode and cast copolyester film then undergoes subsequent processing to manufacture the battery.
It will be appreciated that the preferences and elements described in respect of the first aspect apply equally to the second aspect.
The present invention further provides a film made by the method of the second aspect.
According to a third aspect, there is provided a metal-ion battery (particularly a lithium-ion battery) comprising the copolyester film as described herein, wherein said battery comprises an anode, a cathode and a separator between the anode and the cathode, wherein said separator is the copolyester film as described herein.
During use and operation of the battery, the metal ions present in the copolyester film are mobile, enabling the separator to exhibit the required ionic conductivity between the electrodes.
Preferably, the metal-ion battery is a solid-state battery (also referred to herein as a dry-cell battery). Alternatively, the metal-ion battery further comprises a liquid or gel electrolyte, typically referred to in the art as a wet-cell battery. It will be appreciated by those skilled in the art that the metal-ion battery is a rechargeable battery.
Preferably, the metal-ion battery further comprises an anode current collector and a cathode current collector.
Any suitable anode, anode current collector, cathode and cathode current collector, as conventional in the art, may be used.
Suitable anodes include graphite and/or lithium titanate (LTO).
Suitable cathodes include lithium or mixed oxides of lithium and other metal(s), particularly lithium titanate (LTO), lithium iron phosphate (LiFePO4, also known as LFP) and/or lithium-nickel-manganese-cobalt oxide (LiNiMnCoO2, also known as NMC).
Suitable anode and/or cathode current collectors are disclosed in, for example, UK application no. 2106834.1, the disclosure of which is incorporated herein by reference. In particular, said anode current collector and/or said cathode current collector may be independently selected from current collectors comprising a biaxially oriented polymeric substrate layer (preferably wherein the polymeric substrate layer is polyester, preferably PET or PEN) and a first metal layer on a side of the polymeric substrate layer, wherein the polymeric substrate layer exhibits positive thermal expansion (preferably from greater than 0% to no more than 3.0%, preferably from 0.1% to 2.0%, preferably from 0.2% to 1.5%) in air at 200° C. in each of the transverse direction (TD) and machine direction (MD), wherein the polymeric substrate layer has a thickness of no more than 12 μm (preferably 1.0 to 12.0 μm, preferably 2.0 to 8.0 μm, preferably 4.0 to 8.0 μm, preferably 4.0 to 6.0 μm), and wherein the first metal layer has a thickness of no more than 1000 nm, and preferably wherein the current collector further comprises a second metal layer, wherein the first metal layer and the second metal layer are on opposing sides of the polymeric substrate layer and wherein the second metal layer independently has a thickness of no more than 1000 nm. Preferably, the thickness of the first metal layer and, where present, the second metal layer is each independently from 50 nm to 1000 nm, preferably from 100 nm to 1000 nm, preferably from 100 nm to 800 nm, preferably from 150 nm to 700 nm. The first metal layer and, where present, the second metal layer suitably each independently exhibits isotropic thermal expansion in air at 200° C. of from greater than 0% to no more than 1.0%, preferably from 0.25% to 0.75%, preferably from 0.3% to 0.5%, preferably wherein the first metal layer and the second metal layer exhibit the same thermal expansion at 200° C. as each other. The first metal layer and, where present, the second metal layer each independently comprise at least one of aluminium, copper, nickel, titanium, silver, nickel-copper alloy, or aluminium-zirconium alloy, and preferably wherein the first and second metal layers are selected from the same material, and preferably wherein the first and second metal layers are both either aluminium or copper. Such current collectors preferably exhibit one or more of the following properties:
Such preferred current collectors may be made by a method which comprises the steps of (I) forming a biaxially oriented polymeric substrate layer, and (II) depositing a metal on one or both surfaces of said substrate layer to form a metal layer (preferably using thermal evaporation deposition, electron beam evaporation deposition or virtual cathode deposition). Preferably step (I) comprises the following stages, in order:
It will be appreciated that the term “metal” in the metal layers of said preferred current collectors is used in a context which is distinct and independent from the use of the term “metal” as used in the context of the separators and batteries in the remainder of the present disclosure. In particular, the identity of the metal layer in a current collector is independent from the identity of the metal ions in the separator and the identity of the metal-ion battery (i.e. whether the metal ion battery is a lithium ion battery or a sodium ion battery etc.).
The preferences and elements described in respect of the first and second aspects apply equally to the third aspect.
According to a fourth aspect there is provided the use of the copolyester film as described herein as a separator in a battery, preferably in a metal-ion battery, preferably in a lithium-ion battery.
The preferences and elements described in respect of the first to third aspects apply equally to the fourth aspect.
According to a fifth aspect of the invention, there is provided a method of manufacturing a metal-ion battery comprising the copolyester film as described herein, the method comprising the steps of:
The preferences and elements described in respect of the first to fourth aspects apply equally to the fifth aspect.
The following test methods were used to characterise the properties of the copolyester films, separators and batteries described herein.
(i) Glass Transition Temperature (Tg), Crystalline Temperature (Tc) and Crystalline Melting Point (Tm)
These thermal parameters were measured by differential scanning calorimetry (DSC) using a PerkinElmer HyperDSC 8500. Unless otherwise stated, measurements were made according to the following standard test method and based on the method described in ASTM E1356-98. The sample was maintained under an atmosphere of dry nitrogen for the duration of the scan. A flow rate of 20 ml min−1 and Al pans were used. Samples (5 mg) were initially heated at 20° C. min−1 from 20° C. to 350° C. in order to erase the previous thermal history (1st heating scan). After an isothermal hold at 350° C. for 2 min, samples were cooled at 20° C. min−1 to 20° C. (1st cooling scan). Samples were then reheated at 20° C. min−1 to 350° C. (2nd heating scan). Values of Tg and TM were obtained from 2nd heating scans. As is well known, the glass transition temperature of a polymer is the temperature at which it changes from a glassy, brittle state to a plastic, rubbery state. The value of a Tg was determined as the extrapolated onset temperature of the glass transition observed on the DSC scans (heat flow (W/g) against temperature (° C.)), as described in ASTM E1356-98. It will be appreciated that the copolyesters of the present invention may be associated with two Tg values, one Tg for the soft segments and one Tg for the hard segments. The values of Tc and Tm were determined from the DSC scans as the peak exotherm or endotherm of the transition.
The term “melt viscosity” as used herein means the complex viscosity of a polymer measured at a particular melt temperature and a particular frequency of oscillation. The complex viscosity was measured by rotational rheology testing using a TA Instruments DHR-1 according to the following test method. Polymer samples (2.5 g) were dried under dynamic vacuum at 140° C. for 16 h. The samples were then held between 2×25 mm diameter parallel plates and heated to the required temperature under a nitrogen atmosphere. Analysis of the complex viscosity of the polymer was performed via a temperature ramp method, whereby samples were heated at a rate of 4° C. min−1, at constant strain (5%) and angular frequency (10 rad s−1).
(iii) Through-Film Ionic Conductivity (Dry Cell Setup (Solid State))
The through-film ionic conductivity of film samples with no additional electrolyte present, i.e. in the dry cell setup (solid state), was determined by Electrochemical Impedance Spectroscopy (EIS). Dry coin cells having a diameter of 12 mm were constructed. Dry coin cells having a diameter of 12 mm were constructed. Symmetric Al/Al dry coin cells with 1×1 mm spacers were constructed at a dew point of <40° C. in an argon glove box. AC impedance spectra were obtained using a AutoLab unit under open circuit voltage (OCV) in the AC frequency range from 100 mHz to 1 MHz at an operating temperature of the battery (within the range of about 25° C. and about 75° C., and at ambient temperature (25° C.) unless otherwise specified) following a perturbation voltage of 10 mV. A Nyquist impedance plot was generated and the x-axis intercepts used to calculate resistance values (in ohms) for the resistance R1 of the coin cell components (in ohms) and the bulk resistance R2 of the separator (it will be appreciated that the separator has the relatively higher resistance value of the two values generated form the Nyquist plot). The through-film ionic conductivity (σ) of the film separator was calculated from the bulk resistance R2 using the formula′.
where d is the film sample thickness (in cm) and A is the area of the film (in cm2) contacting the electrodes. It will be appreciated that the area of the film refers to the total film area, i.e. the total area of both sides of the film contacting the Al electrodes. The ionic conductivity is expressed in Siemens/cm, usually in the form of its logarithm (base 10).
GPC measurements were performed on a Malvern/Viscotek TDA 301 using an Agilent PL HFIPgel guard column plus 2×30 cm PL HFIP gel columns. A solution of HFIP with 25 mM NaTFAc was used as eluent, with a nominal flow rate of 0.8 mL min−1. All experimental runs were conducted at ° C., employing a refractive index detector. Molecular weights are referenced to polymethylmethacrylate calibrants. Data capture and subsequent data analysis were carried out using Omnisec software. Samples were prepared at a concentration of 2 mg mL−1, with 20 mg of sample dissolved in 10 mL eluent. These solutions were stirred for 24 h at room temperature and then warmed at 40° C. for 30 mins to fully dissolve the polymer. Each sample was filtered through a 0.45 μm polytetrafluoroethylene membrane prior to injection. Determination of MW may also be made using such a measurement. Once the MW and MN values are known, the PDI may be determined.
Shrinkage was assessed for film samples (preferably having dimensions 200 mm×10 mm) which were cut in specific directions relative to the machine and transverse directions of the film and marked for visual measurement. The longer dimension of the sample (i.e. the 200 mm dimension) corresponds to the film direction for which shrinkage is being tested, i.e. for the assessment of shrinkage in the machine direction, the longer dimension of the test sample is oriented along the machine direction of the film. After heating the specimen to the predetermined temperature (by placing in a heated oven at that temperature) and holding for the predetermined interval, it was cooled to room temperature and its dimensions re-measured manually. The thermal shrinkage was calculated and expressed as a percentage of the original length.
1H NMR spectroscopy was used to determine the level of poly(alkylene oxide) in the copolyester, using an ECS400 spectrometer at 80° C., referenced to residual solvent (d2-TCE (1,1,2,2-tetrachloroethane)) resonances.
(vii) Expansion of the Biaxially Oriented Polymeric Layer (of the Preferred Current Collector)
A sample of the biaxially oriented polymeric layer of the preferred current collector having dimensions of 5 mm×8 mm was subjected to thermomechanical analysis using a thermomechanical analyser (TMA Q400 by TA Instruments Inc.). The longer dimension of the sample (i.e. the 8 mm dimension) corresponds to the sample direction for which expansion was being tested. The sample was mounted on the apparatus and the sample was subjected in the machine direction (MD) or in the transverse direction (TD) to a load of 1 N/mm2 and a temperature increase rate of 10° C./min from 32° C. to 220° C. The thermal expansion in air at a temperature of 200° C. was measured. The thermal expansion in air at 200° C. is defined as the % change of dimension of the film in the given direction (i.e. in the MD or TD), and calculated as (L1−L0)/L0×100, where L0 is the dimension at 32° C. and L1 is the dimension at 200° C. As the skilled person will appreciate, a negative thermal expansion indicates thermal shrinkage.
(viii) Sheet Resistance (of the Preferred Current Collector)
The sheet resistance of the conductive layer of the preferred current collector was measured using a linear four point probe (Jandel Model RM2) according to ASTM F390-98 (2003).
A current collector sample having dimensions 50 mm×10 mm was held at each end between a pair of conducting clamps. The sample was clamped such that 10 mm2 at each end of the sample was held within the clamps. A current was passed through the samples at a ramp rate of 2 A/min until breakdown was observed. The temperature profile of the sample was monitored using a thermal imaging camera throughout the test, in order to determine the temperature at breakdown.
The adhesion strength of the metallised polymeric substrate to an EAA (ethylene acrylic acid film) having a thickness of 25 μm (available commercially as Vistafix(TP) from UCB Sidac Division) was assessed as follows. A sample of the current collector and a sample of the EAA film were positioned together such that the outer surface of the metallised polymeric substrate layer was contacted with the surface of the EAA film. The samples were heat-sealed using a Sentinel Model 12 (Packaging Industries Group Inc) machine under the following conditions: 105° C. (top jaw) and 25° C. (lower jaw) for 10 seconds under a pressure of 50 psi. The sealed sample was cut into 25 mm wide strips and the adhesion strength was determined using an Instron Model 4464. The jaws were set 50 mm apart. The upper jaw held the EAA piece of the sealed sample and travelled up at a speed of 300 mm/min, while the lowerjaw held the current collector piece of the sealed sample and was stationary. The average peel force was measured and reported as a mean value of 5 results. The plane of adhesion failure was also noted. When the adhesion strength between the metal layer and the polymeric substrate layer is lower than the adhesion strength (about 800 g/25 mm) between the metal layer and the EEA film, the test sample delaminates along the interface of the metal layer and polymeric substrate layer. In this case, the average peel force represents the adhesion strength between the metal layer and the polymeric substrate layer. When the adhesion strength between the metal layer and the polymeric substrate layer is higher than the adhesion strength (800 g/25 mm) between the metal layer and the EEA film, the test sample delaminates along the interface of the metal layer and EEA film. A further plane of failure is coherent failure within the metallised layer itself, which also indicates that the adhesion strength between the metal layer and the polymeric substrate layer is greater than the force required to achieve coherent failure (typically the adhesion strength between the metal layer and the polymeric substrate layer is therefore greater than about 800 g/25 mm).
The Ultimate Tensile Strength (UTS), Elongation To Break (ETB) and the F5 value (stress at 5% elongation) are measured according to test method ASTM D882. Using a straight edge and a calibrated sample cutter (10 mm+/−0.5 mm) five strips (100 mm in length) of the film are cut along the machine direction. Each sample is tested using an Instron test machine, using pneumatic action grips with rubber jaw faces. The tests are conducted at ambient conditions. The crosshead speed (rate of separation) is 25 mm·min−1. The strain rate is 50%. Elongation to Break (∈B (%)) is defined as:
where L0 is the original length of the sample between grips.
The brittleness of the film is measured primarily in terms of its ETB value, with a relatively higher ETB value signifying a relatively lower brittleness. As the skilled person would appreciate, a relatively higher ETB value also indicates that the film separators exhibit a relatively higher in-plane flexibility (i.e. flexibility in the plane of the film), and hence improved resistance to the potential dimensional changes of the anode and cathode described hereinabove.
(xii) Flex-Cracking
Flex-cracking can be assessed qualitatively by the repeated bending (through a given angle and about a fulcrum point) of the film, and assessing by eye whether any cracks have developed in the film. A relatively lower degree of flex-cracking signifies that a film has the higher out-of-plane flexibility (i.e. bendability) required for the conditions that the film would be exposed to during cell winding and assembly of batteries.
The present invention is further illustrated with reference to the following non-limiting examples.
In the following discussion, reference to “LICGC” is to a lithium-ion conducting glass ceramic powder available commercially from Ohara under the tradename LICGC™ PW-01, and reference to “PEG3350” is to a polyethylene glycol having a number average molecular weight (MN) of 3350.
A copolyester (P1) was made using ethylene glycol, terephthalic acid and polyethylene glycol (PEG3350). PEG3350 was present at a level of 16.4 wt % of the copolyester.
The copolyesters were made by reacting 5551 g terephthalic acid, 2664 g ethylene glycol and 2006 g PEG3350 under pressure (about 40 psi) at high temperature (about 255° C.), along with the addition of an antioxidant (Irganox® 1010, 7 g). A trace of sodium hydroxide (0.35 g) was added to prevent the formation of unwanted by-products, and the esterification reaction proceeded without the need of a catalyst. Water was distilled off from the reaction and the reaction stopped once 90% of the theoretical weight of water from the reaction had been collected. An antifoam agent (Xiameter™ DC 1510-US, 0.35 g) was then added to minimise material carryover. Polycondensation was then effected with a titanium-based catalyst system (Tyzor® TnBT, 2 g and Tyzor® AC422, 7.1 g) at about 275° C., and wherein the pressure above the melt was reduced to less than 1 mm Hg. As the polycondensation reaction proceeded, the viscosity of the batch increased, and once an appropriate viscosity (suitably from about 50 to about 100 Pa·S) had been achieved the polymerisation reaction was stopped by restoring the pressure in the vessel back to atmosphere. The copolyester was then extruded as a lace and cast into a water bath, dried and pelletized.
A series of copolyester films based on copolyester P1 was made and comprising various additives, as shown in Table 1, which also shows the thickness, ionic conductivity, internal resistance (R1) and bulk resistance (R2) of the final film.
A film was prepared by melt-extruding and casting copolyester P1 to form a cast copolyester film, which was subsequently biaxially drawn using a simultaneous forward and sideways draw ratio of 3.5.
Comparative Example 3 and Example 1 were made by solvent casting techniques after dissolution/dispersion of the film of Comparative Example 2 in N-methyl-2-pyrrolidone (NMP). Specifically, the components shown in Table 1 were dispersed and thoroughly mixed in 5 mL NMP in an autoclave at 160° C. for 24 hours. The resultant copolyester composition was then cast on the surface of an aluminium disc (i.e. the electrode in the test cell) and dried by heating at 60° C. for 24 hours. The dried copolyester was then subjected to vacuum drying at 60° C. for 24 hours to provide the copolyester films.
A further comparative film (Comparative Example 1) comprising LICGC was obtained from Ohara under the tradename LICGC™ AG-01.
A comparison of Example 1 with Comparative Examples 2 and 3 demonstrates that the addition of the ceramic particle material significantly improves the ionic conductivity of the polyester films. Indeed, the film of Example 1 provides an ionic conductivity which is comparable to the ceramic separator of Comparative Example 1, with the advantage of being significantly thinner. Furthermore, the film of Example 1 demonstrated advantageous flexibility compared to Comparative Example 1 which was very brittle and thereby difficult to manufacture and subject to fracture in use. Thus, the film of Example 1 exhibited an advantageous combination of ionic conductivity, flexibility and low thickness for use as a separator in a solid state battery, whilst retaining ease of manufacture.
The copolyester was made using bis(2-hydroxyethyl) isophthalate (BHEI) and polyethylene glycol (PEG 3350). PEG 3350 was present at a level of 50 wt % of the copolyester. The copolyesters were made by reacting 49.82 g BHEI, and 50.18 kg PEG 3350 along with the addition of an antioxidant (Irganox® 1010, 2.95 g). Polycondensation was effected with an antimony trioxide catalyst (0.20 g) at about 280-290° C., and wherein the pressure above the melt was reduced to less than 5 mm Hg. As the polycondensation reaction proceeded, the viscosity of the batch increased, and once a pre-determined viscosity had been achieved the polymerisation reaction was stopped by restoring the pressure in the vessel back to atmosphere. The copolyester was then extruded as a lace, cast into a water bath and dried.
Copolyester P2 was then used to prepare a series of solvent-cast copolyester films (Comparative Examples 4 and 5 and Example 2) containing various additives, as shown in Table 2. The copolyester was dissolved in NMP and the other components shown in Table 2 were introduced, dispersed and thoroughly mixed in NMP in a beaker at 25° C. for 12 hours. Comparative Example 4 used 10 mL NMP, Comparative Example 5 used 0.5 mL NMP whereas Example 2 used 5 mL NMP. Films were made by solvent-casting the resultant copolyester compositions on an aluminium surface and dried by heating at 60° C. for 24 hours, and then vacuum-dried at 60° C. for a further 24 hours to provide the copolyester film. Table 2 shows the thickness, ionic conductivity, internal resistance (R1) and bulk resistance (R2) of the final film.
A comparison of Example 2 with Comparative Examples 4 and 5 demonstrates that the addition of the ceramic particulate material significantly improves the ionic conductivity of the polyester films. The separator of Example 2 provides an ionic conductivity which approaches that of the ceramic separator of Comparative Example 1, with the advantages of being significantly thinner and showing advantageous mechanical properties, in particular flexibility without brittleness.
The ionic conductivity of the films of Comparative Examples 3 and 5, and Examples 1 and 2 was also measured at 40° C. and 60° C., and the results are shown in Table 3, along with the ionic conductivity at 25° C.
The results in Table 3 demonstrate that the addition of the ceramic particle material significantly improves the ionic conductivity of the polyester films at all temperatures tested, and to commercially useful levels of ionic conductivity. Furthermore, the results in Table 3 demonstrate that ionic conductivity can be reliably increased even at elevated temperatures.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2110926.9 | Jul 2021 | GB | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/GB2022/052005 | 7/29/2022 | WO |
