Patent Application
20160126520
The present invention relates to a battery separator including a laminated polyolefin microporous membrane and a method of producing the same.
Nonaqueous electrolyte batteries typified by lithium ion secondary batteries have a high energy density, and thus have been widely used as a power source, for example, for notebook computers, cellular phones, and electric automobiles.
These nonaqueous electrolyte batteries with a high energy density is prone to abnormal heat generation when an internal short circuit occurs, and thus have been required to have a function of preventing a temperature rise above a certain level.
In this regard, microporous membranes composed mainly of polyolefins have been used as a separator to ensure the safety. Polyolefin microporous membranes have shutdown properties such that resin is melted at about 130° C. and blocks pores to shut down the flow of ions, and thus can prevent an abnormal temperature rise in a battery due to an internal short circuit. At this time, it is necessary to block the pores quickly at a certain temperature in order to maintain the safety of the battery.
In addition, polyolefin microporous membranes have been required to be heat-resistant because they shrink and rupture due to a temperature rise in a battery, due to which electrodes can come into contact with each other to cause a short circuit, resulting in abnormal heat generation in the battery.
Furthermore, in nonaqueous electrolyte batteries, in particular, lithium ion batteries, when lithium metal is used as a negative electrode, dendritic lithium metal, as a result of repeated charge and discharge, may precipitate and break through a separator to cause an internal short circuit, and thus polyolefin microporous membranes are required to have physical strength.
In response, investigations have been made to improve heat resistance and/or physical strength by laminating a modifying porous layer comprising a water-soluble resin or water-dispersible resin and fine particles on a polyolefin microporous membrane. However, there is a problem of deterioration of shutdown properties and reduction in air resistance of the polyolefin microporous membrane due to infiltration of the resin component into pores of the membrane. In addition, the resin component sometimes formed a thin film on the surface of the polyolefin microporous membrane to further reduce the air resistance. Furthermore, during the process for laminating a modifying porous layer on the polyolefin microporous membrane, the slitting process, or the battery assembly process, the modifying porous layer can be peeled off, in which case it is difficult to secure the safety.
Patent Document 1 discloses a laminated porous film in which a heat-resistant layer (modifying porous layer) is laminated by applying a slurry comprising 3500 parts by weight of alumina and 100 parts by weight, in terms of sodium carboxymethylcellulose (hereinafter also referred to as “CMC” for short), of CMC solution to the surface of a substrate polyethylene porous film.
Patent Document 2 discloses a nonaqueous electrolyte secondary battery separator obtained by laminating a porous layer comprising 591 g of ion-exchanged water, 9 g of water-soluble polymer CMC, and 45 g of alumina fine particles on a porous polyethylene film. This separator has dimensional stability and load characteristics.
Patent Document 3 discloses that a laminated film comprising a heat-resistant layer composed mainly of a porous polyolefin layer and filler, which is excellent in heat-shrinkable properties and shape retention can be obtained if the overall basis weight of the heat-resistant layer is at least 0.5 times the overall basis weight of the porous polyolefin layer.
Further, Patent Document 4 discloses a polyolefin porous membrane comprising a polyethylene resin and having (a) a shutdown temperature of 135° C. or lower, (b) a rate of air resistance change of 1×104 sec/100 cc/° C. or more, and (c) a transverse shrinkage rate at 130° C. of not more than 20%, and discloses that the polyolefin porous membrane has excellent shutdown properties.
In the laminated microporous membranes disclosed in Patent Documents 1 to 3, it is difficult to maintain the properties of a substrate porous membrane because of infiltration of a water-soluble resin into pores of the membrane, and in particular, the problem is deterioration of shutdown properties at low temperatures. Further, in Patent Document 1, it is intended to maintain the properties of the substrate even in the case where the modifying porous layer comprising a water-soluble resin and particles is laminated on a polyolefin porous membrane, but it is necessary, in applying a slurry, to adjust the contact angle between the slurry and the substrate porous membrane.
On the other hand, the polyolefin microporous membrane disclosed in Patent Document 4 provides a limited improvement in heat resistance and physical strength, and, for example, one possible method is to laminate the modifying porous layer of Patent Documents 1 to 3 on the polyolefin porous membrane of Patent Document 4, but deterioration of shutdown properties cannot be avoided by simple lamination.
In other words, hitherto there has been no laminated polyolefin microporous membrane that is satisfactory in heat resistance and physical strength while utilizing the shutdown properties of a polyolefin microporous membrane.
An object of the present invention is to provide a battery separator comprising a laminated polyolefin microporous membrane composed of a polyolefin microporous membrane and a modifying porous layer having adhesion to the polyolefin microporous membrane, the polyolefin microporous membrane being provided with physical strength and heat resistance with shutdown properties not being significantly reduced, and a method of producing the battery separator.
To solve the problems described above, the battery separator of the present invention has the following constitution:
A battery separator which is a laminated polyolefin microporous membrane, comprising a polyolefin microporous membrane, and a modifying porous layer comprising a water-soluble resin or water-dispersible resin, and fine particles, the modifying porous layer being laminated on at least one surface of the polyolefin microporous membrane, wherein the polyolefin microporous membrane comprises a polyethylene resin and has (a) a shutdown temperature (a temperature at which an air resistance measured while heating the polyolefin microporous membrane at a temperature rise rate of 5° C./min reaches 1×105 sec/100 cc) of 135° C. or lower, (b) a rate of air resistance change (a gradient of a curve representing dependency of the air resistance on temperature at an air resistance of 1×104 sec/100 cc) of 1×104 sec/100 cc/° C. or more, (c) a transverse shrinkage rate at 130° C. (measured by thermomechanical analysis under a load of 2 gf at a temperature rise rate of 5° C./min) of 20% or less, and a thickness of 16 μm or less, the shutdown temperature difference between the polyolefin microporous membrane and the laminated polyolefin microporous membrane being 4.0° C. or less.
In the battery separator of the present invention, the water-soluble resin or water-dispersible resin preferably comprises at least one of carboxymethylcellulose and an acrylic resin.
In the battery separator of the present invention, the fine particles are preferably at least one selected from titanium dioxide, alumina, and boehmite.
In the battery separator of the present invention, the polyethylene resin preferably has a ΔHm≦125° C., a cumulative endotherm up to 125° C. relative to a heat of crystal melting measured by differential scanning calorimetry at a temperature rise rate of 10° C./min, of not more than 20% and a T50%, a temperature at the time when the endotherm reaches 50% of the heat of crystal melting, of 135° C. or lower.
In the battery separator of the present invention, the polyethylene resin preferably comprises a copolymer of ethylene and any other α-olefin.
In the battery separator of the present invention, preferably, the polyethylene resin comprises a copolymer of ethylene and any other α-olefin, and the copolymer is produced using a single-site catalyst and has a mass average molecular weight of not less than 1×104 but less than 7×106.
To solve the problems described above, the method of producing the battery separator of the present invention has the following constitution:
A method of producing the battery separator according to any one of the above, comprising the steps of:
(a) preparing a polyolefin resin solution by melt-kneading a polyolefin resin comprising a polyethylene resin with a membrane-forming solvent in a twin-screw extruder such that the ratio of a feed rate Q (kg/h) of the polyolefin resin to a screw speed Ns (rpm) (Q/Ns) is 0.1 to 0.55 Kg/h/rpm, the polyethylene resin having a ΔHm≦125° C., a cumulative endotherm up to 125° C. relative to a heat of crystal melting measured by differential scanning calorimetry at a temperature rise rate of 10° C./min, of not more than 20% and a T50%, a temperature at the time when the endotherm reaches 50% of the heat of crystal melting, of 135° C. or lower;
(b) forming a gel-like sheet by extruding the polyolefin resin solution through a die and cooling the extrudate;
(c) stretching the gel-like sheet at a rate of 1 to 80%/sec relative to 100% of the length before stretching;
(d) removing the membrane-forming solvent to obtain a polyolefin microporous membrane; and
(e) applying a coating solution comprising a water-soluble resin or water-dispersible resin, and fine particles to at least one surface of the polyolefin microporous membrane obtained above, followed by drying, wherein the volume ratio of the water-soluble resin or water-dispersible resin to the fine particles is 2 to 8% and the concentration of the water-soluble resin or water-dispersible resin is 0.8 to 5%.
The present invention provides a laminated polyolefin microporous membrane having excellent shutdown properties, physical strength, and heat resistance as well as adhesion between a polyolefin microporous membrane and a modifying porous layer. “Modifying porous layer” as used herein refers to a layer comprising a resin that provides or improves at least one properties such as heat resistance, adhesion to electrode material, and electrolyte permeability.
In the present invention, by infiltrating in small amounts a water-soluble resin component or water-dispersible resin component constituting a modifying porous layer into pores of a polyolefin microporous membrane excellent in shutdown properties, heat resistance, and rate of air resistance change produced by using a polyolefin resin having specific properties and a highly-controlled membrane-forming technique, increase in shutdown temperature due to infiltration of the water-soluble resin component or water-dispersible resin component in the modifying porous layer into the microporous membrane can be reduced to a low level. Further, by using a modifying porous layer with heat resistance, a synergistic effect with the excellent heat resistance of the polyolefin microporous membrane is produced, providing a battery separator having more excellent heat resistance. The battery separator of the present invention will be described below, but the present invention is, of course, not limited to this description.
The polyolefin microporous membrane used in the present invention (i) is produced from a polyolefin resin comprising a polyethylene resin having a ΔHm≦125° C., a cumulative endotherm up to 125° C. relative to a heat of crystal melting measured by differential scanning calorimetry at a given temperature rise rate, of not more than 20% and a T50%, a temperature at the time when the endotherm reaches 50% of the heat of crystal melting, of 135° C. or lower, and has excellent heat resistance in a temperature range from a shutdown start temperature to a shutdown temperature and a low shutdown temperature, and (ii) is produced by preparing a polyolefin resin solution by melt-kneading the polyolefin resin comprising the polyethylene resin with a membrane-forming solvent in a twin-screw extruder such that the ratio of a feed rate Q (kg/h) of the polyolefin resin to a screw speed Ns (rpm) (Q/Ns) is 0.1 to 0.55 kg/h/rpm, forming a gel-like sheet by extruding the polyolefin resin solution obtained through a die and cooling the extrudate, and removing the membrane-forming solvent from the gel-like sheet obtained, and has high physical stability before the start of shutdown, a high rate of air resistance change after the start of shutdown, excellent heat resistance in a temperature range from a shutdown start temperature to a shutdown temperature, and a low shutdown temperature. It was discovered that through the use of the above polyolefin microporous membrane, deterioration of shutdown properties of the polyolefin membrane is reduced even if a modifying porous layer with excellent heat resistance is laminated, and an excellent battery separator is produced.
Thus, the polyolefin microporous membrane used in the present invention is characterized by comprising a polyethylene resin and having (a) a shutdown temperature (a temperature at which an air resistance measured while heating the polyolefin microporous membrane at a temperature rise rate of 5° C./min reaches 1×105 sec/100 cc) of 135° C. or lower, (b) a rate of air resistance change (a gradient of a curve representing dependency of the air resistance on temperature at an air resistance of 1×104 sec/100 cc) of 1×104 sec/100 cc/° C. or more, (c) a transverse shrinkage rate at 130° C. (measured by thermomechanical analysis under a load of 2 gf at a temperature rise rate of 5° C./min) of 20% or less, and a thickness of 16 μm or less, the shutdown temperature difference between the polyolefin microporous membrane and the laminated polyolefin microporous membrane being 4.0° C. or less.
The method of producing the polyolefin microporous membrane used in the present invention is characterized by comprising (1) preparing a polyolefin resin solution by melt-kneading a polyolefin resin comprising a polyethylene resin with a membrane-forming solvent in a twin-screw extruder such that the ratio of a feed rate Q (kg/h) of the polyolefin resin to a screw speed Ns (rpm) (Q/Ns) is 0.1 to 0.55 kg/h/rpm, the polyethylene resin having a ΔHm≦125° C., a cumulative endotherm up to 125° C. relative to a heat of crystal melting measured by differential scanning calorimetry at a temperature rise rate of 10° C./min, of not more than 20% and a T50%, a temperature at the time when the endotherm reaches 50% of the heat of crystal melting, of 135° C. or lower, (2) forming a gel-like sheet by extruding the polyolefin resin solution through a die and cooling the extrudate, (3) stretching the gel-like sheet, (4) and then removing the membrane-forming solvent.
The polyolefin microporous membrane used in the present invention will be described in detail.
The polyolefin resin constituting the polyolefin microporous membrane used in the present invention comprises a polyethylene resin described below.
For the polyethylene resin used as a raw material in the present invention, the percentage of a cumulative endotherm up to 125° C. relative to a heat of crystal melting ΔHm measured by differential scanning calorimetry (DSC) at a temperature rise rate of 10° C./min (hereinafter referred to as ΔHm≦125° C.) is preferably not more than 20%, and the temperature at the time when the endotherm reaches 50% of the heat of crystal melting ΔHm (hereinafter referred to as T50%) is preferably 135° C. or lower.
ΔHm≦125° C. is a parameter affected by molecular weight, degree of branching, and degree of molecular entanglement of polyethylene. A ΔHm≦125° C. of not more than 20% leads to a low shutdown temperature, which provides excellent heat resistance in a temperature range from a shutdown start temperature to a shutdown temperature. ΔHm≦125° C. is more preferably 17% or less.
T50% is a parameter affected by configuration of primary structures (e.g., molecular weight, molecular weight distribution, degree of branching, molecular weight of branched chains, distribution of branching points, and percentage of copolymers) and higher-order structures (e.g., crystal size, crystal distribution, and crystal lattice regularity) of polyethylene [homopolymer or ethylene/α-olefin copolymer (the same applies hereinafter)], and is an indicator of shutdown temperature and the rate of air resistance change after the start of shutdown. When T50% is 135° C. or lower, the polyolefin microporous membrane, when used as a battery separator, exhibits low and good shutdown properties and an excellent shutdown response at overheating.
The heat of crystal melting ΔHm (J/g) of the polyethylene resin is determined by the following procedure in accordance with JIS K 7122. First, a polyethylene resin sample (a molded product obtained by melt-pressing at 210° C. (thickness: 0.5 mm)) is placed in a sample holder of a differential scanning calorimeter (Pyris Diamond DSC available from Perkin Elmer, Inc.), heat-treated at 230° C. for 1 minute in a nitrogen atmosphere, cooled to 30° C. at 10° C./min, kept at 30° C. for 1 minute, and heated to 230° C. at a speed of 10° C./min. As shown in
The polyethylene resin may be a single substance or a composition of two or more polyethylenes as long as its ΔHm≦125° C. and T50% are within the above ranges. The polyethylene resin is preferably (a) an ultra-high molecular weight polyethylene, (b) a polyethylene other than ultra-high molecular weight polyethylenes, or (c) a mixture of an ultra-high molecular weight polyethylene with a polyethylene other than ultra-high molecular weight polyethylenes (polyethylene composition). In every case, the mass average molecular weight (Mw) of the polyethylene resin, though not critical, is preferably 1×104 to 1×107, more preferably 5×104 to 15×106, and particularly preferably 1×105 to 5×106.
The ultra-high molecular weight polyethylene has a Mw of 7×105 or more. The ultra-high molecular weight polyethylene may be not only an ethylene homopolymer but also an ethylene/α-olefin copolymer containing a small amount of other α-olefins. Preferred examples of α-olefins other than ethylene include propylene, butene-1, pentene-1, hexene-1, 4-methylpentene-1, octene-1, vinyl acetate, methyl methacrylate, and styrene. The Mw of the ultra-high molecular weight polyethylene is preferably 1×106 to 15×106, more preferably 1×106 to 5×106.
(b) Polyethylene Other than Ultra-High Molecular Weight Polyethylenes
The polyethylene other than ultra-high molecular weight polyethylenes has a Mw of not less than 1×104 but less than 7×105. At least one selected from the group consisting of high density polyethylene, medium density polyethylene, branched low density polyethylene, and linear low density polyethylene is preferred, and high density polyethylene is more preferred. The polyethylene having a Mw of not less than 1×104 but less than 7×105 may be not only an ethylene homopolymer but also a copolymer containing a small amount of other α-olefins such as propylene, butene-1, and hexene-1. Such a copolymer is preferably produced using a single-site catalyst. The polyethylene other than ultra-high molecular weight polyethylenes is not limited to a single substance and may be a mixture of two or more polyethylenes other than ultra-high molecular weight polyethylenes.
The case where a polyethylene composition is used as the polyethylene resin will be described. The polyethylene composition is a mixture of an ultra-high molecular weight polyethylene with a Mw of 7×105 or more and a polyethylene other than ultra-high molecular weight polyethylenes with a Mw of not less than 1×104 but less than 7×105. The ultra-high molecular weight polyethylene and the polyethylene other than ultra-high molecular weight polyethylenes may be the same as described above. The molecular weight distribution (mass average molecular weight/number average molecular weight (Mw/Mn)) of this polyethylene composition can be easily controlled depending on the intended use. The polyethylene composition is preferably a composition of the above ultra-high molecular weight polyethylene and a high density polyethylene. The Mw of the high density polyethylene used in the polyethylene composition is preferably not less than 1×105 but less than 7×105, more preferably 1×105 to 5×105, and most preferably 2×105 to 4×105. The content of the ultra-high molecular weight polyethylene in the polyethylene composition is preferably 1% by mass or more based on 100% by mass of the total polyethylene composition, more preferably 2 to 50% by mass. The molecular weight distribution (mass average molecular weight/number average molecular weight (Mw/Mn)) of the polyethylene composition can be easily controlled depending on the intended use.
Mw/Mn is a measure of molecular weight distribution, and larger values indicate wider molecular weight distributions. The Mw/Mn of the polyethylene resin is not critical, but in every case where the polyethylene resin is one of the (a) to (c) above, it is preferably 5 to 300, more preferably 10 to 100.
The polyethylene resins as described above may be a commercially available product. Examples of the commercially available product include Nipolon Hard (registered trademark) 6100A, 7300A, and 5110A (all available from Tosoh Corporation), and HI-ZEX (registered trademark) 640UF and 780UF (all available from Prime Polymer Co., Ltd.).
The polyethylene resin may be a composition comprising a polyolefin other than polyethylene resins or a resin other than polyolefins as long as the effects of the present invention are not compromised. Therefore, it should be understood that the term “polyethylene resin” includes not only polyethylene but also resins other than polyethylene. The polyolefin other than polyethylene resins can be at least one selected from the group consisting of polypropylene, polybutene-1, polypentene-1, polyhexene-1, poly-4-methylpentene-1, polyoctene-1, polyvinyl acetate, polymethyl methacrylate, polystyrene, and ethylene/α-olefin copolymer, each having a Mw of 1×104 to 4×106, and a polyethylene wax having a Mw of 1×103 to 1×104. Polypropylene, polybutene-1, polypentene-1, polyhexene-1, poly-4-methylpentene-1, polyoctene-1, polyvinyl acetate, polymethyl methacrylate, and polystyrene may be not only a homopolymer but also a copolymer containing other α-olefins.
Examples of the resin other than polyethylene resins include heat resistant resins having a melting point or a glass transition temperature (Tg) of 150° C. or higher. The heat resistant resin is preferably a crystalline resin (including partially crystalline resins) having a melting point of 150° C. or higher and an amorphous resin having a Tg of 150° C. or higher. The melting point and Tg can be measured according to JIS K 7121, and so on.
The method of producing the polyolefin microporous membrane used in the present invention comprises the steps of (1) preparing a polyolefin resin solution by melt-kneading the above polyolefin resin and a membrane-forming solvent, (2) extruding the polyolefin resin solution through a die, (3) forming a gel-like sheet by cooling the extrudate, (4) stretching, (5) removing the membrane-forming solvent, and (6) drying. In other words, it is a production process what is called Wet process. Between the steps (5) and (6), any of (7) hot roll treatment, (8) hot solvent treatment, and (9) heat-setting may be optionally conducted. Furthermore, after the step (6), (10) stretching a microporous membrane, (11) heat treatment, (12) cross-linking with ionizing radiation, (13) hydrophilization, and the like can be conducted.
The polyolefin resin solution is prepared by adding an appropriate membrane-forming solvent to the polyolefin resin mentioned above and then melt-kneading the resulting mixture. To the polyolefin resin solution, the various additives described above such as inorganic fillers, antioxidants, UV absorbers, antiblocking agents, pigments, and dyes can be optionally added as long as the effects of the present invention are not compromised. For example, fine silicate powder can be added as a pore-forming agent.
The membrane-forming solvent can be a liquid solvent or a solid solvent. Examples of liquid solvents include aliphatic or cyclic hydrocarbons such as nonane, decane, decalin, paraxylene, undecane, dodecane, and liquid paraffin; and mineral oil distillates having a boiling point equivalent to those of these hydrocarbons. To obtain a gel-like sheet with a stable solvent content, it is preferable to use a nonvolatile liquid solvent such as liquid paraffin. The solid solvent preferably has a melting point of 80° C. or lower, and examples of such solid solvents include paraffin wax, ceryl alcohol, stearyl alcohol, and dicyclohexyl phthalate. The liquid solvent and the solid solvent may be used in combination.
The viscosity of the liquid solvent is preferably 30 to 500 cSt at 25° C., more preferably 30 to 200 cSt.
The melt-kneading method, though not critical, is preferably uniform kneading in an extruder. This method is suitable for preparing a high-concentration polyethylene resin solution. The melt-blending temperature is generally from (the melting point Tm of the polyethylene resin+10° C.) to (Tm+110° C.) though it may be properly set depending on the components of the polyolefin resin. In cases where the polyethylene resin is (a) an ultra-high molecular weight polyethylene, (b) a polyethylene other than ultra-high molecular weight polyethylenes, or (c) a polyethylene composition, the melting point Tm of the polyethylene resin is a melting point of them. In the case of a polyethylene composition comprising a polyolefin other than polyethylene resins or a heat resistant resin, the melting point Tm of the polyethylene resin is a melting point of an ultra-high molecular weight polyethylene, a polyethylene other than ultra-high molecular weight polyethylenes, or a polyethylene composition contained in the above composition, and so on.
The extruder is preferably a twin-screw extruder. The twin-screw extruder may be an intermeshing co-rotating twin-screw extruder, an intermeshing counter-rotating twin-screw extruder, a non-intermeshing co-rotating twin-screw extruder, or a non-intermeshing counter-rotating twin-screw extruder. The intermeshing co-rotating twin-screw extruder is preferred because it has a self-cleaning function and can achieve a higher rotation speed with a smaller load than those of counter-rotating twin-screw extruders.
In the method of producing the battery separator of the present invention, when introducing the polyethylene resin into the twin-screw extruder, the ratio of a feed rate Q of the polyethylene resin (kg/h) to a screw speed Ns (rpm) (Q/Ns) is 0.1 to 0.55 kg/h/rpm. If Q/Ns is less than 0.1 kg/h/rpm, the polyolefin resin will experience excessive shear failure, resulting in a low meltdown temperature, which leads to poor rupture resistance during the temperature rising after shutdown. If Q/Ns is more than 0.55 kg/h/rpm, uniform kneading cannot be achieved. Q/Ns is more preferably 0.2 to 0.5 kg/h/rpm. The screw speed Ns is more preferably 250 rpm or more. The upper limit of the screw speed Ns, though not critical, is preferably 500 rpm.
The concentration of the polyethylene resin is preferably 10 to 50% by mass based on 100% by mass of the total of the polyethylene resin and the membrane-forming solvent, more preferably 20 to 45% by mass.
The melt-kneaded polyethylene resin solution is extruded from an extruder through a die directly or after being pelletized. When using a sheet-forming die having a rectangular orifice, the die typically has a gap of 0.1 to 5 mm and is heated to 140 to 250° C. during extrusion. The extrusion speed of the heated solution is preferably 0.2 to 15 m/min.
A gel-like sheet is formed by cooling the extrudate from the die. The cooling is preferably conducted at least to a gelation temperature at a speed of 50° C./min or higher. Such cooling fixes a structure in which the polyethylene resin is microphase-separated by the membrane-forming solvent (a gel structure comprising a polyethylene resin phase and a membrane-forming solvent phase). The cooling is preferably conducted to 25° C. or lower.
The cooling roll temperature is preferably from (the crystallization temperature Tc of the polyethylene resin−120° C.) to (Tc−5° C.), more preferably from (Tc−115° C.) to (Tc−15° C.). A cooling roll temperature in this preferred range enables sufficiently rapid cooling. In cases where the polyethylene resin is (a) the ultra-high molecular weight polyethylene, (b) the polyethylene other than ultra-high molecular weight polyethylenes, or (c) the polyethylene composition described above, the crystallization temperature Tc of the polyolefin resin is a crystallization temperature of them. In cases where the polyolefin resin is a composition comprising a polyolefin other than polyethylene or a heat resistant resin, the crystallization temperature Tc of the polyolefin resin is a crystallization temperature of an ultra-high molecular weight polyethylene, a polyethylene other than ultra-high molecular weight polyethylenes, or a polyethylene composition contained in the above composition, and so on. “Crystallization temperature” herein refers to a value determined according to JIS K 7121. The ultra-high molecular weight polyethylene, the polyethylene other than ultra-high molecular weight polyethylenes, and the polyethylene composition generally have a crystallization temperature of 110 to 115° C. Accordingly, the cooling roll temperature is set in the range of −10 to 105° C., preferably in the range of −5° C. to 95° C. The contact time of the cooling roll and the sheet is preferably 1 to 30 seconds, more preferably 2 to 15 seconds.
The gel-like sheet before washing is preferably stretched in at least one direction. After heating, the gel-like sheet is preferably stretched to a predetermined magnification by a tenter method or a roll method. The gel-like sheet can be uniformly stretched because it contains a membrane-forming solvent. The stretching improves mechanical strength and expands pores, which is particularly preferred in the use as a battery separator. Although the stretching may be monoaxial stretching or biaxial stretching, the biaxial stretching is preferred. The biaxial stretching may be simultaneous biaxial stretching, sequential stretching, or multi-stage stretching (e.g., a combination of simultaneous biaxial stretching and sequential stretching), but the simultaneous biaxial stretching is particularly preferred.
The stretching magnification, in the case of monoaxial stretching, is preferably 2× or more, more preferably 3 to 30×. In the case of biaxial stretching, it is preferably at least 3× in both directions, i.e., 9× or more in area magnification.
The stretching temperature is preferably not higher than the melting point Tm of the polyolefin resin+10° C., more preferably in the range of not lower than the crystal dispersion temperature Tcd described above but lower than the melting point Tm described above. When the stretching temperature is in this preferred range, the polyethylene resin does not melt, and molecular chains can be sufficiently oriented as a result of stretching; furthermore, the polyethylene resin softens so sufficiently that the membrane is less likely to be broken by stretching, which enables a stretching at a high magnification. “Crystal dispersion temperature” herein refers to a value determined by measuring temperature characteristics of dynamic viscoelasticity in accordance with ASTM D4065. The ultra-high molecular weight polyethylene, the polyethylene other than ultra-high molecular weight polyethylenes, and the polyethylene composition described above have a crystal dispersion temperature of about 90 to 100° C., and accordingly, the stretching temperature is preferably in the range of 90 to 140° C., more preferably in the range of 100 to 130° C.
In the method of producing the battery separator of the present invention, the stretching speed is 1 to 80%/sec. In the case of monoaxial stretching, it is 1 to 80%/sec in the longitudinal direction (MD) or the transverse direction (TD). In the case of biaxial stretching, it is 1 to 80%/sec in both MD and TD. The stretching speed (%/sec) of the gel-like sheet is expressed as a percentage relative to 100% of the length before stretching. A stretching speed of less than 1%/sec results in unstable stretching. A stretching speed of more than 80%/sec leads to reduced heat resistance. The stretching speed is more preferably 2 to 70%/sec. In the case of biaxial stretching, the stretching speeds in MD and TD may be the same or different as long as they are 1 to 80%/sec, though they are preferably the same.
The stretching described above causes cleavage between polyethylene crystal lamellas, and the polyethylene phase (ultra-high molecular weight polyethylene, polyethylene other than ultra-high molecular weight polyethylenes, or polyethylene composition) becomes finer, forming large numbers of fibrils. The resulting fibrils form a three-dimensional network structure (three-dimensionally and irregularly connected network structure).
Depending on the desired physical properties, stretching can be conducted with a temperature distribution in the membrane thickness direction, whereby a microporous membrane with more excellent mechanical strength is provided. A method therefor is described specifically in Japanese Patent No. 3347854.
A washing solvent is used to remove the membrane-forming solvent. Since the polyethylene resin phase in the gel-like sheet is separated from the membrane-forming solvent phase, removing the membrane-forming solvent provides a microporous membrane. The removal of the membrane-forming solvent can be conducted using a known washing solvent. Examples of washing solvents include volatile solvents, such as saturated hydrocarbons such as pentane, hexane, and heptane; chlorinated hydrocarbons such as methylene chloride and carbon tetrachloride; ethers such as diethyl ether and dioxane; ketones such as methyl ethyl ketone; linear fluorocarbons such as trifluoroethane, C6F14, and C7F16; cyclic hydrofluorocarbons such as C5H3F7; hydrofluoroethers such as C4F9OCH3 and C4F9OC2H5; and perfluoroethers such as C4F9OCF3 and C4F9OC2F5. These washing solvents have a low surface tension (e.g., 24 mN/m or less at 25° C.). Using a washing solvent having a low surface tension prevents a micropore-forming network structure from shrinking because of a surface tension at gas-liquid interfaces during drying after washing, thereby providing a microporous membrane having a high porosity and high permeability.
Membrane washing can be conducted by immersion in a washing solvent, showering a washing solvent, or the combination thereof. The washing solvent is preferably used in an amount of 300 to 30,000 parts by mass based on 100 parts by mass of the membrane before washing. Washing with a washing solvent is preferably conducted until the amount of the remaining membrane-forming solvent is reduced to less than 1% by mass of the amount initially added.
The polyolefin microporous membrane obtained by washing is dried, for example, by heat-drying or air-drying to completely remove the solvent.
The drying temperature is preferably equal to or lower than the crystal dispersion temperature Tcd of the polyolefin resin, particularly preferably 5° C. or more lower than the Tcd. As described above, the polyethylene resin has a crystal dispersion temperature of about 90 to 100° C.
The drying is preferably conducted until the amount of the remaining washing solvent is reduced to 5% by mass or less based on 100% by mass of the microporous membrane (dry weight), more preferably to 3% by mass or less. If the drying is insufficient, the porosity of the microporous membrane is reduced when heat treatment is conducted subsequently, resulting in poor permeability, which is not preferred.
At least one surface of the gel-like sheet may be brought into contact with a heat roll, whereby the compression resistance of the microporous membrane is improved. A specific method therefor is described, for example, in JP 2006-248582 A.
The gel-like sheet may be brought into contact with a hot solvent, whereby a microporous membrane with more excellent mechanical strength and permeability is provided. A method therefor is described specifically in WO 2000/20493.
The stretched gel-like sheet may be heat-set. A specific method therefor is described, for example, in JP 2002-256099 A.
The dried polyolefin microporous membrane may be stretched in at least one direction as long as the effects of the present invention are not compromised. This stretching can be conducted while heating the membrane by a tenter method or the like similarly to the above.
The temperature for stretching the microporous membrane is preferably not higher than the melting point Tm of the polyethylene resin, more preferably in the range of the Tcd to the Tm described above. Specifically, it is in the range of 90 to 135° C., and preferably in the range of 95 to 130° C. In the case of biaxial stretching, the magnification is preferably 1.1 to 2.5× in at least one direction, more preferably 1.1 to 2.0×.
The dried membrane is preferably heat-set and/or relaxed by a known method. The heat-setting or relaxing may be properly selected depending on the physical properties the polyolefin microporous membrane requires. The heat treatment stabilizes crystals and makes lamellas uniform. It is particularly preferable to relax the microporous membrane after stretching once.
The dried polyolefin microporous membrane may be cross-linked by irradiation with ionizing radiation such as alpha-rays, beta-rays, gamma-rays, or electron beams. In the case of irradiation with electron beams, the electron dose of 0.1 to 100 Mrad is preferred, and the accelerating voltage of 100 to 300 kV is preferred. The cross-linking increases the meltdown temperature of the microporous membrane.
The dried polyolefin microporous membrane may be hydrophilized by monomer-grafting treatment, surfactant treatment, corona-discharging treatment, plasma treatment, or the like using a known method.
According to this process, a polyolefin microporous membrane is provided having high physical stability before the start of shutdown, a high rate of air resistance change after the start of shutdown, which is an indicator of shutdown speed, excellent heat resistance in a temperature range from a shutdown start temperature to a shutdown temperature, and a low shutdown temperature.
The modifying porous layer in the present invention will now be described. It is important for the modifying porous layer in the present invention to contain a water-soluble resin or water-dispersible resin, and fine particles. Using a water-soluble resin or water-dispersible resin and fine particles not only provides excellent heat resistance but also leads to reduced cost, and, further, is preferred also from the standpoint of environmental load during a production process.
Specific examples of the water-soluble resin or water-dispersible resin include CMC, polyvinyl alcohol, and acrylic resins such as polyacrylic acid, polyacrylamide, and polymethacrylic acid, and CMC and acrylic resins are most preferred. The acrylic resin may be a commercially available acrylic emulsion, and specific examples thereof include “ACRYSET” (registered trademark) TF-300 (available from Nippon Shokubai Co., Ltd.) and “Polysol” (registered trademark) AP-4735 (available from Showa Denko K.K.).
The modifying porous layer can comprise various additives such as surfactants and antistatic agents as components other than the water-soluble resin or water-dispersible resin as long as the object of the present invention can be achieved.
The fine particles are preferably inorganic particles. Examples of inorganic particles include calcium carbonate, calcium phosphate, amorphous silica, crystalline glass filler, kaolin, talc, titanium dioxide, alumina, silica-alumina composite oxide particles, barium sulfate, calcium fluoride, lithium fluoride, zeolite, molybdenum sulfide, mica, and boehmite. Of these, titanium dioxide, alumina, and boehmite are suitable because they are available at low cost.
The average diameter of the fine particles is preferably 1.5 times to 50 times the average pore diameter of the polyolefin microporous membrane, more preferably 2.0 times to 20 times. When the average diameter of the particles is in this preferred range, a significant increase in air resistance due to blocking of the pores of the polyolefin microporous membrane is prevented, and also serious defects in a battery due to falling off of the particles during a battery assembly process can be prevented effectively. The shape of the particles may be spherical, substantially spherical, plate-like, or needle-like, but is not limited thereto.
In the production method of the present invention, through the process of applying a solution containing a water-soluble resin or water-dispersible resin, fine particles, and a solvent (hereinafter also referred to as “coating solution”) to a polyolefin microporous membrane and removing the solvent by drying or the like, the membrane comprising the water-soluble resin or water-dispersible resin, and the fine particles, when the coating solution applied is dried, forms voids around the fine particles to become a porous membrane. If the solution containing a water-soluble resin does not contain fine particles, a porous membrane may not be formed.
To maintain the shutdown properties of the polyolefin microporous membrane, the upper limit of the volume percentage of the water-soluble resin or water-dispersible resin relative to the solid component of the modifying porous layer is 8%, preferably 7%, and the lower limit of the volume percentage is 2%, preferably 3%. When the volume percentage of the water-soluble resin or water-dispersible resin relative to the solid component of the modifying porous layer is more than 8%, there is a problem of deterioration of shutdown properties, and when the volume percentage is less than 2%, there is a problem of the modifying porous layer having reduced membrane strength and being easily peeled off
However, sufficient adhesion between the polyolefin microporous membrane and the modifying porous layer may not be provided only by adjusting the volume percentage of the resin relative to the solid component of the modifying porous layer to be in the range described above. Thus, in the present invention, the upper limit of the resin concentration in the coating solution described above is 5.0% by weight, preferably 2% by weight, and the lower limit is 0.8% by weight, preferably 1.5% by weight. When the resin concentration is more than 5.0% by weight, there is a problem of air resistance being likely to be low, and when the resin concentration is less than 0.8% by weight, there is a problem of reduction in adhesion between the modifying porous layer and the polyolefin membrane.
In the present invention, the term “solvent” includes not only liquids that dissolve water-soluble resin or water-dispersible resin but also, in a broad sense, dispersion media used to disperse water-soluble resin or water-dispersible resin into particles. The solvent in the present invention is mainly water. In the present invention, it is preferable to use ion-exchanged water or distilled water. The solvent may be water alone, and a water-soluble organic solvent such as alcohols can be optionally used in combination. The use of a water-soluble organic solvent improves the drying speed and coating properties. A preferred water-soluble organic solvent is a mixed solution containing an alcohol such as ethanol, isopropyl alcohol, or benzyl alcohol in an amount in the range of 0.1 to 10% by mass based on the total coating solution. In addition, an organic solvent other than alcohols can be added in an amount less than 1% by mass to the extent that it can be dissolved. However, the total amount of the alcohol and the other organic solvent is preferably less than 10% by mass of the coating solution. Furthermore, components other than the fine particles and the water-soluble resin or water-dispersible resin can be optionally added as long as the object of the present invention can be achieved. Examples of such components include dispersants and pH adjusters.
The thickness of the modifying porous layer is preferably 1 to 5 μm, more preferably 1 to 4 μm, and most preferably 1 to 3 μm. When the thickness of the modifying porous layer is in this preferred range, sufficient adhesion to electrodes is provided, and the membrane strength and insulation properties of the polyolefin microporous membrane can be ensured when it melts and shrinks at or higher than its melting point; a sufficient pore-blocking function is provided, and an abnormal reaction can be prevented; the size when taken up will not be too large, which is suitable for the increase in battery capacity which is expected to progress in the future; and curling is unlikely to increase, which contributes to improved productivity in a battery assembly process.
The porosity of the modifying porous layer is preferably 30 to 90%, more preferably 40 to 70%. When the porosity of the modifying porous layer is in this preferred range, the laminated polyolefin microporous membrane (battery separator) obtained by laminating the modifying porous layer has low electrical resistance, which makes it easy to apply a high current, and the membrane strength is maintained.
The upper limit of the total thickness of the laminated polyolefin microporous membrane obtained by laminating the modifying porous layer is preferably 35 μm, more preferably 20 μm. The lower limit is preferably not lower than 6 μm, more preferably not lower than 9 μm. When the total thickness of the laminated polyolefin microporous membrane is in this preferred range, a mechanical strength and insulation properties sufficient for a battery separator can be ensured, and in addition, the area of electrodes that can be loaded into a container can be prevented from decreasing, which results in avoidance of decrease in capacity.
The modifying porous layer is preferably laminated by applying the coating solution mentioned above to the polyolefin microporous membrane. Examples of the method of applying the coating solution include reverse roll coating, gravure coating, kiss coating, roll brushing, spray coating, air knife coating, meyer bar coating, pipe doctor method, blade coating, and die coating, and these methods can be used alone or in combination. In this case, it is preferable to apply the coating solution to the lower surface of the polyolefin microporous membrane being conveyed horizontally. As a result of applying to the lower surface, resin components which have a relatively low specific gravity tends to be located at the interface with the polyolefin microporous membrane, which facilitates adhesion.
The solvent is typically removed by drying. The solvent in the coating can also be removed by, before drying, immersing a laminated product obtained by coating the polyolefin microporous membrane with the coating solution in a liquid of greater volatility than water that does not dissolve the water-soluble resin or water-dispersible resin, and replacing the liquid with the solvent. When the coating solution is applied to the upper surface of the polyolefin microporous membrane, the drying temperature is preferably a temperature which does not decrease air permeability; specifically, it is 100° C. or lower, preferably 90° C. or lower, and more preferably 80° C. or lower. Examples of the liquid of greater volatility than water include alcohols such as ethanol, isopropyl alcohol, and benzyl alcohol.
The battery separator of the present invention is desirably stored dry, but when it is difficult to store it absolutely dry, it is preferable to perform a vacuum drying treatment at 100° C. or lower immediately before use.
The battery separator of the present invention can be used as a separator for batteries such as secondary batteries such as nickel-hydrogen batteries, nickel-cadmium batteries, nickel-zinc batteries, silver-zinc batteries, lithium ion secondary batteries, and lithium polymer secondary batteries, and is preferably used particularly as a separator for lithium ion secondary batteries.
The polyolefin microporous membrane used as a substrate of the laminated polyolefin microporous membrane of the present invention has the following physical properties.
The shutdown temperature of the polyolefin microporous membrane used in the present invention is 135° C. or lower. If it is higher than 135° C., when the modifying porous layer is laminated on the polyolefin microporous membrane, the resulting battery separator may have a low shutdown response at overheating.
The rate of air resistance change after the start of shutdown of the polyolefin microporous membrane used in the present invention is 1×104 sec/100 cc/° C. or more, preferably 1.2×104 sec/100 cc/° C. or more. If the rate of air resistance change is less than 1×104 sec/100 cc/° C., when the modifying porous layer is laminated on the polyolefin microporous membrane, the resulting battery separator has a high shutdown temperature.
The transverse shrinkage rate at 130° C. (measured by thermomechanical analysis under a load of 2 gf at a temperature rise rate of 5° C./min) of the polyolefin microporous membrane used in the present invention is 20% or less. If it is more than 20%, when the modifying porous layer is laminated on the polyolefin microporous membrane, the resulting battery separator has significantly reduced heat resistance. This heat shrinkage rate is preferably 17% or less.
The thickness of the polyolefin microporous membrane used as a substrate of the laminated polyolefin microporous membrane of the present invention is 16 μm or less. The upper limit is preferably 12 μm, more preferably 10 μm. The lower limit of the thickness of the polyolefin microporous membrane is preferably 5 μm, more preferably 6 μm. If the thickness of the polyolefin microporous membrane is more than 16 μm, the area per unit volume of a battery case is significantly restricted, which is not suitable for the increase in the capacity of a battery which is expected to progress in the future. When the lower limit of the thickness of the polyolefin microporous membrane is in this preferred range, it is easy to provide a membrane strength and pore-blocking function of practical use.
The upper limit of the air resistance of the polyolefin microporous membrane used in the present invention is preferably 400 sec/100 cc Air, more preferably 350 sec/100 cc Air, and still more preferably 150 sec/100 cc Air. The lower limit is preferably 50 sec/100 cc Air, more preferably 70 sec/100 cc Air, and still more preferably 100 sec/100 cc Air. When the air resistance of the polyolefin microporous membrane is in this preferred range, functions of a battery can be fully exerted since the battery is provided with sufficient charge and discharge properties, in particular, sufficient ion permeability (charge and discharge operating voltage) and lifetime (closely related to the amount of electrolytic solution retained), and in addition, a sufficient mechanical strength and insulation properties are provided, which eliminates the possibility of a short circuit during charge and discharge.
For the porosity of the polyolefin microporous membrane used in the present invention, the upper limit is preferably 70%, more preferably 60%, and still more preferably 55%. The lower limit is preferably 30%, more preferably 35%, and still more preferably 40%.
When the porosity of the polyolefin microporous membrane is in this preferred range, functions of a battery can be fully exerted since the battery is provided with sufficient charge and discharge properties, in particular, sufficient ion permeability (charge and discharge operating voltage) and lifetime (closely related to the amount of electrolytic solution retained), and in addition, a sufficient mechanical strength and insulation properties are provided, which eliminates the possibility of a short circuit during charge and discharge.
The tensile rupture strength of the polyolefin microporous membrane used in the present invention is preferably 80,000 kPa or more in both MD and TD. When it is 80,000 kPa or more, the membrane will not rupture when used as a battery separator. The tensile rupture strength is more preferably 100,000 kPa or more.
The tensile rupture elongation of the polyolefin microporous membrane used in the present invention is preferably 100% or more in both MD and TD. When the tensile rupture elongation is 100% or more, the membrane will not rupture when used as a battery separator.
The shutdown start temperature of the polyolefin microporous membrane used in the present invention is preferably 130° C. or more. When the shutdown start temperature of the polyolefin microporous membrane is in this preferred range, the polyolefin microporous membrane, when used as a lithium battery separator, shows sufficiently high shutdown response at overheating.
The meltdown temperature of the polyolefin microporous membrane used in the present invention is preferably 150° C. or higher. The meltdown temperature of the laminated polyolefin microporous membrane is preferably 200° C. or higher. When the meltdown temperature of the polyolefin microporous membrane and the meltdown temperature of the laminated polyolefin microporous membrane are each in these preferred ranges, good rupture resistance is exhibited during the temperature rising after shutdown.
The average pore size of the polyolefin microporous membrane used in the present invention has a great influence on shutdown properties and the like, and therefore is preferably 0.05 to 0.30 μm, more preferably 0.07 to 0.50 μm, and still more preferably 0.08 to 0.13 μm. When the average pore size of the polyolefin microporous membrane is in this preferred range, the water-soluble resin or water-dispersible resin easily infiltrates into the pores of the polyolefin microporous membrane, which provides sufficient adhesion to the modifying porous layer and excellent electrolyte permeability, and in addition, shutdown properties will not be reduced.
The rate of air resistance increase of the laminated polyolefin microporous membrane is preferably 135% or less, more preferably 130% or less. The rate of air resistance increase of the laminated polyolefin microporous membrane is a ratio (expressed as a percentage) of the air resistance of the laminated polyolefin microporous membrane to the air resistance of the polyolefin microporous membrane.
“Shutdown temperature difference” refers to a value obtained by subtracting the shutdown temperature of the polyolefin microporous membrane from the shutdown temperature of the laminated polyolefin microporous membrane. In the present invention, the shutdown temperature difference is 4.0° C. or less. The shutdown temperature difference is preferably 3.0° C. or less. When the shutdown temperature difference is more than 4.0° C., the shutdown response at overheating of the polyolefin microporous membrane is slow, which may compromise the safety of batteries typified by lithium ion secondary batteries.
(3) Adhesion between Modifying Porous Layer and Polyolefin Microporous Membrane
The adhesion between the modifying porous layer and the polyolefin microporous membrane is preferably 0.8 or more, more preferably 1.0 or more. “Adhesion” as used herein refers to a value measured by the measurement method of (11) Peeling Strength between Modifying Porous Layer and Polyolefin Microporous Membrane described below.
The polyolefin microporous membrane used in the present invention has an excellent balance of shutdown properties, heat resistance in a temperature range from a shutdown start temperature to a shutdown temperature, and meltdown properties, and also is excellent in permeability and mechanical properties.
The present invention will now be described in detail by way of example, but the present invention is not limited to these examples. The measurements in the examples are values determined by the following methods.
For a polyolefin microporous membrane and a battery separator, the thickness of a 10-cm square sample was measured at 10 randomly selected points with a contact thickness meter, and its average value was used as an average thickness (μm).
Using an Oken-type air resistance meter EGO-1T (manufactured by Asahi Seiko Co., Ltd.), samples of a polyolefin microporous membrane and a battery separator were each fixed such that wrinkling did not occur, and an air resistance was measured in accordance with JIS P 8117. The sample was 10-cm square, and measuring points were the center and four corners, five points in total, of the sample; its average value was used as an air resistance p (sec/100 cc Air). When the length of a side of the sample is less than 10 cm, measurements at five points at intervals of 5 cm may be used. The rate of air resistance increase was determined by dividing the air resistance of the battery separator by the air resistance of the polyolefin microporous membrane and expressed as %.
A maximum load was measured when a microporous membrane having a thickness T1 (μm) was pricked with a needle of 1 mm in diameter with a spherical end surface (radius R of curvature: 0.5 mm) at a speed of 2 mm/sec. The measured maximum load La was converted to a maximum load Lb at a thickness of 20 μm by the equation: Lb=(La×20)/T1, which was used as a pin puncture strength (Mn/20 μm).
Measurements were made using a strip test piece with a width of 10 mm according to ASTM D882.
For a shutdown temperature TSD (° C.), the air resistance of a polyolefin microporous membrane was measured using an Oken-type air resistance meter EGO-1T (manufactured by Asahi Seiko Co., Ltd.) while heating the polyolefin microporous membrane at a temperature rise rate of 5 C.°/min, and a temperature at which the air resistance reached 1×105 sec/100 cc which is the detection limit was determined, which temperature was used as a shutdown temperature T (° C.).
The data of the air resistance p (sec/100 cc Air) at a temperature T (° C.), which was obtained in the above shutdown temperature measurement, was used to generate a curve (shown in
The data of the air resistance p at a temperature T, which was obtained in the above shutdown temperature measurement, was used to generate a temperature-air resistance curve (shown in
Using a thermomechanical analyzer TMA/SS6000 (manufactured by Seiko Instruments, Inc.), a test piece of 10 mm (TD)×3 mm (MD) was heated from room temperature at a speed of 5° C./min while drawing the test piece in the longitudinal direction under a load of 2 g, and a rate of dimensional change from the size at 23° C. was measured at 130° C. three times. The measurements were averaged to determine a shrinkage rate.
After the above shutdown temperature TSD was reached, heating was further continued at a temperature rise rate of 5° C./min, and a temperature at which the air resistance became 1×105 sec/100 cc again was determined and used as a meltdown temperature TMD (° C.) (see
The heat resistances of a polyolefin microporous membrane and a battery separator were each determined from the average value of the rate of change from the initial size in MD and TD after storage in an oven at 130° C. for 60 minutes.
(11) Peeling Strength between Modifying Porous Layer and Polyolefin Microporous Membrane
Adhesive tape No. 405 (available from Nichiban Co., Ltd., 24 mm wide) was applied to a modifying porous layer side of a separator obtained in Examples and Comparative Examples, and the separator was cut to 24 mm in width and 150 mm in length to prepare a test sample. A peeling strength at the interface between the modifying porous layer and a polyolefin microporous membrane was measured by the peeling method (peel rate: 500 mm/min, T-peel) under the conditions of 23° C. and 50% RH using a tensile tester “Tensilon” (registered trademark)®-100 (manufactured by A & D Company, Limited). Measurements were made over time within 100 mm from the start to the end of the measurements, and an average value of the measurements was calculated and converted to a value per 25 mm width, which was used as a peeling strength. At the peeling interface, the modifying porous layer surface can remain on the polyolefin microporous membrane side, but also in this case, a value was calculated as a peeling strength between the modifying porous layer and the polyolefin microporous membrane.
The rate of air resistance increase of a laminated polyolefin microporous membrane is a ratio (expressed as a percentage) of the air resistance of the laminated polyolefin microporous membrane to the air resistance of a polyolefin microporous membrane.
Rate of air resistance increase (%)=(air resistance of laminated polyolefin microporous membrane/air resistance of laminated polyolefin microporous membrane)×100
The shutdown temperature difference is expressed as a value obtained by subtracting the shutdown temperature of a polyolefin microporous membrane from the shutdown temperature of a laminated polyolefin microporous membrane.
One hundred parts by mass of a polyethylene (PE) composition comprising 30% by mass of an ultra-high molecular weight polyethylene (UHMWPE) having a mass average molecular weight (Mw) of 2.5×106 and 70% by mass of a high density polyethylene (HDPE) having a Mw of 2.8×105 was dry-blended with 0.375 parts by mass of tetrakis[methylene-3-(3,5-ditertiarybutyl-4-hydroxyphenyl)-propionate]methane to obtain a mixture.
The Mws of UHMWPE and HDPE were determined by gel permeation chromatography (GPC) under the following conditions, and so on.
Measuring apparatus: GPC-150C available from Waters Corporation
Column: “Shodex” (registered trademark) UT806M available from Showa Denko K.K.
Column Temperature: 135° C.
Solvent (mobile phase): o-dichlorobenzene
Solvent flow rate: 1.0 mL/min
Sample Concentration: 0.1% by mass (dissolution conditions: 135° C./h)
Injection amount: 500 μL
Detector: Differential refractometer available from Waters Corporation
Calibration curve: Generated from a calibration curve of a monodisperse polystyrene standard sample using a predetermined conversion constant.
Twenty-five parts by mass of the mixture obtained was charged into a strong-kneading twin-screw extruder (feed rate Q of the polyethylene composition: 54 kg/h). Seventy-five parts by mass of liquid paraffin was fed to the twin-screw extruder via a side feeder, and melt-blended at a temperature of 210° C. while keeping the screw speed Ns at 180 rpm (Q/Ns: 0.3 kg/h/rpm) to prepare a polyethylene solution.
The polyethylene solution obtained was fed from the twin-screw extruder to a T-die, and extruded into a sheet shape. The extrudate was cooled by taking it up around a cooling roll controlled at 50° C. to form a gel-like sheet. The gel-like sheet obtained was simultaneously biaxially stretched 5× at a speed of 20%/sec in both MD and TD with a batch-type stretching machine at 116° C. The gel-like sheet was then re-stretched in TD at 127° C. at a stretching magnification of 1.4× to obtain a gel-like sheet. This gel-like sheet was fixed to a frame plate (size: 30 cm×30 cm, made of aluminum) and immersed in a washing bath of methylene chloride controlled at 25° C., and washed while being swayed at 100 rpm for 3 minutes to remove the liquid paraffin. The washed membrane was air-dried at room temperature, fixed to a tenter, and heat-set at 127° C. for 10 minutes to produce a polyolefin microporous membrane (a) having a thickness of 9 μm.
To 0.8 parts by mass of CMC, product No. 2200, (available from Daicel Finechem Ltd.), 60.8 parts by mass of a solvent was added and stirred for 2 hours. Subsequently, 38.4 parts by mass of alumina fine particles of substantially spherical shape having an average diameter of 0.5 μm were added and stirred for 2 hours to thoroughly disperse the alumina fine particles. The resulting mixture was then microfiltered through a polypropylene felt filter with a filtering particle size (initial filtration efficiency: 95%) of 10 μm to prepare a coating solution (A). At this time, the volume ratio of the resin component to the fine particles was 5:95 (calculated with the specific gravity of CMC as 1.6 g/cm3 and the specific gravity of alumina 4.0 g/cm3).
The coating solution (A) was applied to the lower surface of the polyolefin microporous membrane (a) being conveyed horizontally by gravure coating and dried in a hot-air drying furnace (temperature: 60° C.) for 20 seconds to produce a battery separator with a final thickness of 11 μm.
Similarly to Example 1, the polyolefin microporous membrane (a) was used.
To 1.0 parts by mass of CMC, product No. 2200, (available from Daicel Finechem Ltd.), 50.0 parts by mass of a solvent was added and stirred for 2 hours. Subsequently, 49.0 parts by mass of alumina fine particles of substantially spherical shape having an average diameter of 0.5 μm were added and stirred for 2 hours to thoroughly disperse the alumina fine particles. The resulting mixture was then microfiltered through a polypropylene felt filter with a filtering particle size (initial filtration efficiency: 95%) of 10 μm to prepare a coating solution (B). At this time, the volume ratio of the resin component to the fine particles was 5:95.
The coating solution (B) was applied to the polyolefin microporous membrane (a) in the same manner as in Example 1 and dried to produce a battery separator.
Similarly to Example 1, the polyolefin microporous membrane (a) was used.
To 1.2 parts by mass of CMC, product No. 2200, (available from Daicel Finechem Ltd.), 41.2 parts by mass of a solvent was added and stirred for 2 hours. Subsequently, 57.6 parts by mass of alumina fine particles of substantially spherical shape having an average diameter of 0.5 μm were added and stirred for 2 hours to thoroughly disperse the alumina fine particles. The resulting mixture was then microfiltered through a polypropylene felt filter with a filtering particle size (initial filtration efficiency: 95%) of 10 μm to prepare a coating solution (C). At this time, the volume ratio of the resin component to the fine particles was 5:95.
The coating solution (C) was applied to the polyolefin microporous membrane (a) in the same manner as in Example 1 and dried to produce a battery separator.
Similarly to Example 1, the polyolefin microporous membrane (a) was used.
To 1.5 parts by mass of CMC, product No. 2200, (available from Daicel Finechem Ltd.), 28.6 parts by mass of a solvent was added and stirred for 2 hours. Subsequently, 70.0 parts by mass of alumina fine particles of substantially spherical shape having an average diameter of 0.5 μm were added and stirred for 2 hours to thoroughly disperse the alumina fine particles. The resulting mixture was then microfiltered through a polypropylene felt filter with a filtering particle size (initial filtration efficiency: 95%) of 10 μm to prepare a coating solution (D). At this time, the volume ratio of the resin component to the fine particles was 5:95.
The coating solution (D) was applied to the polyolefin microporous membrane (a) in the same manner as in Example 1 and dried to produce a battery separator.
Similarly to Example 1, the polyolefin microporous membrane (a) was used.
To 1.8 parts by mass of CMC, product No. 2200, (available from Daicel Finechem Ltd.), 13.0 parts by mass of a solvent was added and stirred for 2 hours. Subsequently, 85.2 parts by mass of alumina fine particles of substantially spherical shape having an average diameter of 0.5 μm were added and stirred for 2 hours to thoroughly disperse the alumina fine particles. The resulting mixture was then microfiltered through a polypropylene felt filter with a filtering particle size (initial filtration efficiency: 95%) of 10 μm to prepare a coating solution (E). At this time, the volume ratio of the resin component to the fine particles was 5.0:95.0.
The coating solution (E) was applied to the polyolefin microporous membrane (a) in the same manner as in Example 1 and dried to produce a battery separator.
Similarly to Example 1, the polyolefin microporous membrane (a) was used.
To 2.0 parts by mass of CMC, product No. 2200, (available from Daicel Finechem Ltd.), 39.4 parts by mass of a solvent was added and stirred for 2 hours. Subsequently, 58.6 parts by mass of alumina fine particles of substantially spherical shape having an average diameter of 0.5 μm were added and stirred for 2 hours to thoroughly disperse the alumina fine particles. The resulting mixture was then microfiltered through a polypropylene felt filter with a filtering particle size (initial filtration efficiency: 95%) of 10 μm to prepare a coating solution (F). At this time, the volume ratio of the resin component to the fine particles was 7.9:92.1.
The coating solution (F) was applied to the polyolefin microporous membrane (a) in the same manner as in Example 1 and dried to produce a battery separator.
Similarly to Example 1, the polyolefin microporous membrane (a) was used.
To 2.4 parts by mass of CMC, product No. 2200, (available from Daicel Finechem Ltd.), 28.6 parts by mass of a solvent was added and stirred for 2 hours. Subsequently, 69.1 parts by mass of alumina fine particles of substantially spherical shape having an average diameter of 0.5 μm were added and stirred for 2 hours to thoroughly disperse the alumina fine particles. The resulting mixture was then microfiltered through a polypropylene felt filter with a filtering particle size (initial filtration efficiency: 95%) of 10 μm to prepare a coating solution (G). At this time, the volume ratio of the resin component to the fine particles was 7.9:92.1.
The coating solution (G) was applied to the polyolefin microporous membrane (a) in the same manner as in Example 1 and dried to produce a battery separator.
Similarly to Example 1, the polyolefin microporous membrane (a) was used.
To 6.3 parts by mass of “ACRYSET” (registered trademark) TF-300 (available from Nippon Shokubai Co., Ltd.) (solid component: 40%), 48.0 parts by mass of a solvent was added and stirred for 2 hours. Subsequently, 64.2 parts by mass of alumina fine particles of substantially spherical shape having an average diameter of 0.5 μm were added and stirred for 2 hours to thoroughly disperse the alumina fine particles. The resulting mixture was then microfiltered through a polypropylene felt filter with a filtering particle size (initial filtration efficiency: 95%) of 10 μm to prepare a coating solution (H). At this time, the volume ratio of the resin component to the fine particles was 8:92.
The coating solution (H) was applied to the polyolefin microporous membrane (a) in the same manner as in Example 1 and dried to produce a battery separator.
In producing a polyolefin microporous membrane, the same procedure as in Example 1 was repeated to produce a polyolefin microporous membrane (b), except for using a polyethylene composition comprising 30% by mass of an UHMWPE having a Mw of 2.0×106 and 70% by mass of a HDPE having a Mw of 2.8×105.
The coating solution (D) was applied to the polyolefin microporous membrane (b) in the same manner as in Example 1 and dried to produce a battery separator.
One hundred parts by mass of a polyethylene (PE) composition comprising 30% by mass of an ultra-high molecular weight polyethylene (UHMWPE) having a mass average molecular weight (Mw) of 2.5×106 and 70% by mass of a high density polyethylene (HDPE) having a Mw of 3.0×105 was dry-blended with 0.375 parts by mass of tetrakis[methylene-3-(3,5-ditertiarybutyl-4-hydroxyphenyl)-propionate]methane to obtain a mixture.
Twenty-five parts by mass of the mixture obtained was charged into a strong-kneading twin-screw extruder (feed rate Q of the polyethylene composition: 120 kg/h). Seventy-five parts by mass of liquid paraffin was fed to the twin-screw extruder via a side feeder, and melt-blended at a temperature of 210° C. while keeping the screw speed Ns at 400 rpm (Q/Ns: 0.3 kg/h/rpm) to prepare a polyethylene solution.
The polyethylene solution obtained was fed from the twin-screw extruder to a T-die, and extruded into a sheet shape. The extrudate was cooled by taking it up around a cooling roll controlled at 50° C. to form a gel-like sheet. The gel-like sheet obtained was simultaneously biaxially stretched 5× at a speed of 20%/sec in both MD and TD with a batch-type stretching machine at 114° C. to obtain a gel-like sheet. This gel-like sheet was fixed to a frame plate (size: 30 cm×30 cm, made of aluminum) and immersed in a washing bath of methylene chloride controlled at 25° C., and washed while being swayed at 100 rpm for 3 minutes to remove the liquid paraffin. The washed membrane was air-dried at room temperature, fixed to a tenter, and heat-set at 126° C. for 10 minutes to produce a polyolefin microporous membrane (d) having a thickness of 16 μm.
The coating solution (D) was applied to the polyolefin microporous membrane (d) in the same manner as in Example 1 and dried to produce a battery separator.
One hundred parts by mass of a polyethylene (PE) composition comprising 20% by mass of an ultra-high molecular weight polyethylene (UHMWPE) having a mass average molecular weight (Mw) of 2.5×106 and 80% by mass of a high density polyethylene (HDPE) having a Mw of 3.0×105 was dry-blended with 0.375 parts by mass of tetrakis[methylene-3-(3,5-ditertiarybutyl-4-hydroxyphenyl)-propionate]methane to obtain a mixture. The PE composition comprising the UHMWPE and the HDPE had a ΔHm≦125° C. of 16% and a T50% of 132.9° C.
Twenty-five parts by mass of the mixture obtained was charged into a strong-kneading twin-screw extruder (feed rate Q of the polyethylene composition: 72 kg/h). Seventy-five parts by mass of liquid paraffin was fed to the twin-screw extruder via a side feeder, and melt-blended at a temperature of 210° C. while keeping the screw speed Ns at 240 rpm (Q/Ns: 0.3 kg/h/rpm) to prepare a polyethylene solution.
The polyethylene solution obtained was fed from the twin-screw extruder to a T-die, and extruded into a sheet shape. The extrudate was cooled by taking it up around a cooling roll controlled at 50° C. to form a gel-like sheet. The gel-like sheet obtained was simultaneously biaxially stretched 5× at a speed of 20%/sec in both MD and TD with a batch-type stretching machine at 118° C. to obtain a gel-like sheet. This gel-like sheet was fixed to a frame plate (size: 30 cm×30 cm, made of aluminum) and immersed in a washing bath of methylene chloride controlled at 25° C., and washed while being swayed at 100 rpm for 3 minutes to remove the liquid paraffin. The washed membrane was air-dried at room temperature, fixed to a tenter, and heat-set at 119° C. for 10 minutes to produce a polyolefin microporous membrane (e) having a thickness of 12 μm.
The coating solution (D) was applied to the polyolefin microporous membrane (e) in the same manner as in Example 1 and dried to produce a battery separator.
In producing a polyolefin microporous membrane, the same procedure as in Example 1 was repeated to produce a polyolefin microporous membrane (f), except that a polyethylene composition with a ΔHm≦125° C. of 16% and a T50% of 132.9° C. comprising 20% by mass of an UHMWPE having a Mw of 2.5×106 and 80% by mass of a HDPE having a Mw of 3.0×105 was used, and a gel-like sheet was stretched at 114° C.
The coating solution (D) was applied to the polyolefin microporous membrane (f) in the same manner as in Example 1 and dried to produce a battery separator.
A modifying porous layer was not laminated, and the polyolefin microporous membrane (a) was used as a battery separator.
Similarly to Example 1, the polyolefin microporous membrane (a) was used.
To 6.0 parts by mass of CMC, product No. 2200, (available from Daicel Finechem Ltd.), 50.0 parts by mass of a solvent was added and stirred for 2 hours. Subsequently, 44.0 parts by mass of alumina fine particles of substantially spherical shape having an average diameter of 0.5 μm were added and stirred for 2 hours to thoroughly disperse the alumina fine particles. The resulting mixture was then microfiltered through a polypropylene felt filter with a filtering particle size (initial filtration efficiency: 95%) of 10 μm to prepare a coating solution (I). At this time, the volume ratio of the resin component to the fine particles was 25.4:74.6.
The coating solution (I) was applied to the polyolefin microporous membrane (a) in the same manner as in Example 1 and dried to produce a battery separator.
In producing a polyolefin microporous membrane, 100 parts by mass of a polyethylene (PE) composition comprising 20% by mass of an UHMWPE having a Mw of 2.5×106 and 80% by mass of a HDPE having a Mw of 3.0×105 was dry-blended with 0.375 parts by mass of tetrakis[methylene-3-(3,5-ditertiarybutyl-4-hydroxyphenyl)-propionate]methane to obtain a mixture. The PE composition had a ΔHm≦125° C. of 21% and a T50% of 132.2° C.
The same procedure as in Example 1 was repeated to produce a polyolefin microporous membrane (g), except that 25 parts by mass of the mixture obtained was charged into a strong-kneading twin-screw extruder (feed rate Q of the polyethylene composition: 54 kg/h); 75 parts by mass of liquid paraffin was fed to the twin-screw extruder via a side feeder and melt-blended at a temperature of 210° C. while keeping the screw speed Ns at 720 rpm (Q/Ns: 0.075 kg/h/rpm) to prepare a polyethylene solution; a gel-like sheet was stretched at 114° C.; and the heat-setting temperature was 120° C.
The coating solution (D) was applied to the polyolefin microporous membrane (g) in the same manner as in Example 1 and dried to produce a battery separator.
In producing a polyolefin microporous membrane, the same procedure as in Example 1 was repeated to produce a polyolefin microporous membrane (c), except that a polyethylene composition comprising 20% by mass of an UHMWPE having a Mw of 2.5×106 and 80% by mass of a HDPE having a Mw of 3.0×105 was used; the stretching speed was 100%; re-stretching was not carried out; and the heat-setting temperature was 120° C.
The coating solution (D) was applied to the polyolefin microporous membrane (c) in the same manner as in Example 1 and dried to produce a battery separator.
The resin composition, membrane-forming conditions, and physical properties of the polyolefin microporous membranes produced in Examples 1 to 12 and Comparative Examples 1 to 4 are shown in Table 1, and the physical properties of the battery separators are shown in Table 2 and 3. Notes (1) to (3) in Tables 1 to 3 are described below.
(1) Mw represents a mass average molecular weight.
(2) Q represents a feed rate of a polyethylene composition into a twin-screw extruder, and Ns represents a screw speed.
(3) The difference between the shutdown temperature of a polyolefin microporous membrane and the shutdown temperature of a battery separator.
Table 1 shows that the polyolefin microporous membranes of Examples 1 to 13 have shutdown properties, i.e., a shutdown start temperature of not higher than 130° C., a shutdown speed of not less than 10,000 sec/100 cc/° C., and a shutdown temperature of not higher than 135° C., and are also excellent in permeability and mechanical strength. It can be seen that the laminated polyolefin microporous membranes (battery separators) obtained by laminating a modifying porous layer on these polyolefin microporous membranes have a shutdown temperature that is slightly different from the shutdown temperature of the polyolefin microporous membrane and have an extremely high heat resistance.
On the other hand, the battery separator of Comparative Example 1 has poor properties since a modifying porous layer is not laminated. The battery separators of Comparative Examples 2 to 3 are poor in any one of shutdown properties, permeability, and physical strength.
The battery separator according to the present invention are excellent in shutdown properties, heat resistance, and physical strength, and can be suitably used as a nonaqueous electrolyte battery separator, in particular, a lithium ion secondary battery separator.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2013-179078 | Aug 2013 | JP | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/JP2014/072154 | 8/25/2014 | WO | 00 |
