WO2007060991A1 - ポリオレフィン微多孔膜及びその製造方法、並びに電池用セパレータ及び電池 - Google Patents
ポリオレフィン微多孔膜及びその製造方法、並びに電池用セパレータ及び電池 Download PDFInfo
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- WO2007060991A1 WO2007060991A1 PCT/JP2006/323317 JP2006323317W WO2007060991A1 WO 2007060991 A1 WO2007060991 A1 WO 2007060991A1 JP 2006323317 W JP2006323317 W JP 2006323317W WO 2007060991 A1 WO2007060991 A1 WO 2007060991A1
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- microporous membrane
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M10/00—Secondary cells; Manufacture thereof
- H01M10/42—Methods or arrangements for servicing or maintenance of secondary cells or secondary half-cells
- H01M10/4235—Safety or regulating additives or arrangements in electrodes, separators or electrolyte
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- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
- C08J9/00—Working-up of macromolecular substances to porous or cellular articles or materials; After-treatment thereof
- C08J9/22—After-treatment of expandable particles; Forming foamed products
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- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
- C08J5/00—Manufacture of articles or shaped materials containing macromolecular substances
- C08J5/20—Manufacture of shaped structures of ion-exchange resins
- C08J5/22—Films, membranes or diaphragms
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- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
- C08J9/00—Working-up of macromolecular substances to porous or cellular articles or materials; After-treatment thereof
- C08J9/26—Working-up of macromolecular substances to porous or cellular articles or materials; After-treatment thereof by elimination of a solid phase from a macromolecular composition or article, e.g. leaching out
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M10/00—Secondary cells; Manufacture thereof
- H01M10/05—Accumulators with non-aqueous electrolyte
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M50/00—Constructional details or processes of manufacture of the non-active parts of electrochemical cells other than fuel cells, e.g. hybrid cells
- H01M50/40—Separators; Membranes; Diaphragms; Spacing elements inside cells
- H01M50/409—Separators, membranes or diaphragms characterised by the material
- H01M50/411—Organic material
- H01M50/414—Synthetic resins, e.g. thermoplastics or thermosetting resins
- H01M50/417—Polyolefins
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M50/00—Constructional details or processes of manufacture of the non-active parts of electrochemical cells other than fuel cells, e.g. hybrid cells
- H01M50/40—Separators; Membranes; Diaphragms; Spacing elements inside cells
- H01M50/489—Separators, membranes, diaphragms or spacing elements inside the cells, characterised by their physical properties, e.g. swelling degree, hydrophilicity or shut down properties
- H01M50/491—Porosity
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M50/00—Constructional details or processes of manufacture of the non-active parts of electrochemical cells other than fuel cells, e.g. hybrid cells
- H01M50/40—Separators; Membranes; Diaphragms; Spacing elements inside cells
- H01M50/489—Separators, membranes, diaphragms or spacing elements inside the cells, characterised by their physical properties, e.g. swelling degree, hydrophilicity or shut down properties
- H01M50/494—Tensile strength
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M10/00—Secondary cells; Manufacture thereof
- H01M10/05—Accumulators with non-aqueous electrolyte
- H01M10/052—Li-accumulators
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M10/00—Secondary cells; Manufacture thereof
- H01M10/24—Alkaline accumulators
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
- Y02E60/10—Energy storage using batteries
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/249921—Web or sheet containing structurally defined element or component
Definitions
- Polyolefin microporous membrane Method for producing the same, battery separator and battery
- the present invention relates to a polyolefin microporous membrane, a method for producing the same, a battery separator, and a battery.
- the stability of physical properties until the start of shutdown and the rate of change in air permeability after the start of shutdown are high.
- the present invention relates to a polyolefin microporous membrane having excellent heat shrinkage resistance in a temperature range up to a temperature, having a low shutdown temperature, a method for producing the same, a battery separator, and a battery.
- Polyethylene microporous membranes are mainly used as battery separators.
- separators for lithium-ion batteries have the property that the pores are blocked by the heat generated by the battery, which is not only due to excellent mechanical characteristics and permeability (stopping characteristics), but also when the temperature exceeds the shutdown temperature. Properties that prevent film formation (meltdown properties) are also required.
- Patent No. 2132327 is a polyolefin microporous membrane having excellent strength and permeability, containing 1% by weight or more of ultrahigh molecular weight polyolefin having a mass average molecular weight (Mw) of 7 ⁇ 10 5 or more, and a molecular weight distribution [mass average Molecular weight Z number average molecular weight (MwZMn)] is made of a polyolefin yarn having a composition of 10 to 300, a porosity of 35 to 95%, an average through hole diameter of 0.001 to 0.2 / ⁇ ⁇ , and a width of 15 mm. Proposes a breaking strength of 0.2 kg or more.
- Japanese Patent Application Laid-Open No. 2004-196870 describes a polyolefin microporous membrane comprising polyethylene and polypropylene having a mass average molecular weight of 5 ⁇ 10 5 or more and a heat of fusion measured by a scanning differential calorimeter of 90 jZg or more.
- Japanese Patent Laid-Open No. 2004-196871 has a melting point measured by a scanning differential calorimeter at a temperature rising rate of 3 to 20 ° C. Zmin with polyethylene and a mass average molecular weight of 5 ⁇ 10 5 or more.
- the polyolefin microporous membranes of JP-A-2004-196870 and JP-A-2004-196871 are It has a shutdown temperature of 120-140 ° C and a meltdown temperature of 165 ° C or higher, and has excellent mechanical properties and permeability.
- WO 97Z23554 is a high-density polyethylene microporous film having high resistance and short-circuit resistance (shutdown characteristics).
- the density of terminal vinyl groups by infrared spectroscopy is 2 or more per 10,000 carbon atoms.
- the object of the present invention is to provide a shutdown start temperature (pore size) at which the rate of change in the air permeability after the start of shutdown, which is one of the indices of physical property stability and shutdown speed, is high.
- Polyolefin microporous membrane having excellent heat shrinkage resistance in the temperature range up to shutdown temperature (temperature at which pore clogging is almost completed), low and shutdown temperature, its manufacturing method, and It is to provide a battery separator and a battery.
- the present inventors have (1) a portion of the crystal melting calorie measured by differential scanning calorimetry at a predetermined heating rate that has absorbed heat at 125 ° C. or lower.
- the temperature at which the temperature at which the heat of crystal melting reaches 50% is less than 135 ° C and the polyolefin resin containing polyethylene resin, and the temperature at which the shutdown is initiated is also the temperature from the shutdown temperature to the shutdown temperature.
- Excellent heat-shrinkage resistance in the range, low shutdown temperature, and a polyolefin microporous membrane can be obtained.
- a biaxial extrusion of a polyolefin resin containing the polyethylene-based resin and a film-forming solvent can be obtained.
- the polyolefin microporous membrane of the present invention contains a polyethylene-based resin, and (a) the air permeability measured while heating at a heating rate of 5 ° C / min is 1 X 10 5 sec / 100 The shutdown temperature obtained as the temperature reaching cm 3 is 135 ° C or less, and (b) the air permeability on the curve representing the dependence of the air permeability on the temperature is 1 X 10 4 sec / 100 cm 3 The rate of change of air permeability obtained as the gradient at the coordinates of 1 x 10 4 sec / 100 cm 3 Z ° C or higher, and (c) by thermomechanical analysis with a load of 2 gf and a temperature increase rate of 5 ° C Zmin. The measured lateral shrinkage at 130 ° C is less than 20%.
- the polyethylene-based resin is a fraction of the heat absorbed at 125 ° C or less of the heat of crystal melting measured by differential scanning calorimetry at a constant heating rate within a range of 3 to 20 ° CZmin. Is 20% or less, and the temperature when the heat of crystal fusion reaches 50% is preferably 135 ° C or less.
- the method for producing a polyolefin microporous membrane of the present invention has an endotherm at or below 125 ° C of the heat of crystal melting measured by differential scanning calorimetry at a constant rate of temperature rise in the range of 3 to 20 ° C Zmin.
- the ratio of the formed portion is 20% or less, and when the heat of crystal fusion reaches 50%, the polyolefin resin containing polyethylene resin having a temperature of 135 ° C.
- the ratio of the amount of polyolefin resin input Q (kg / h) to the screw rotation speed Ns (rpm) in the extruder is melt-kneaded so that QZNs is 0.1 to 0.55 kgZhZipm to prepare a polyolefin resin solution.
- the polyolefin resin solution is extruded from a die and cooled to form a gel-like sheet. After the obtained gel-like sheet is stretched, the film-forming solution is removed.
- the gel-like sheet is preferably stretched at a speed of 1 to 80% Z seconds in the stretching axis direction, with the length in the stretching axis direction before stretching being 100%.
- the battery separator of the present invention is formed of the polyolefin microporous film.
- the battery of the present invention comprises a battery separator comprising the polyolefin microporous film.
- the temperature stability range until the shutdown temperature is high the stability of physical properties until the start of shutdown, and the rate of change in air permeability after the start of shutdown, which is one of the indicators of the shutdown speed.
- a polyolefin microporous membrane having excellent heat shrinkage resistance, low temperature and shutdown temperature, and excellent permeability and mechanical properties can be obtained.
- the polyolefin microporous membrane of the present invention is used as a battery separator, a battery excellent in safety and productivity can be obtained.
- FIG. 1 is a graph showing an example of a typical melting endotherm curve.
- FIG. 2 A graph showing the same portion of the melting endotherm curve as in Fig. 1 where the proportion of the portion of the crystal melting heat absorbed at 125 ° C or less is 20% or less.
- FIG. 3 is a graph showing the temperature T (50%) when the heat of crystal fusion reaches 50% of the same melting endothermic curve as in FIG.
- FIG. 4 A graph showing a typical example of a temperature T— (air permeability p) — 1 curve for determining the shutdown start temperature.
- FIG. 5 is a graph showing a typical example of a temperature T—air permeability P curve for determining a shutdown temperature, a rate of change in air permeability, and a meltdown temperature.
- the polyolefin resin that forms the polyolefin microporous membrane of the present invention contains the polyethylene resin described below.
- Polyethylene resin is the part of the heat absorbed at 125 ° C or below of the heat of crystal melting ⁇ H measured by differential scanning calorimetry (DSC) analysis at a constant rate of temperature rise in the range of 3-20 ° CZmin.
- the proportion of minutes (hereinafter referred to as “ ⁇ ⁇ ( ⁇ 125 ° C)”) is 20% or less, and the heat of crystal fusion ⁇ ⁇ is mm
- T (50%) The temperature when it reaches 50% (hereinafter referred to as “T (50%)”) is 135 ° C or less.
- T (50%) is polyethylene [homopolymer or ethylene ' ⁇ -olefin copolymer (hereinafter the same)] molecular weight, molecular weight distribution, degree of branching, molecular weight of branched chain, distribution of branching points, It is a parameter that is affected by the primary structure such as fraction, and the shape of the higher order structure such as crystal size and distribution, crystal lattice regularity, etc., and is an indicator of the shutdown temperature and the rate of change in air permeability after the start of shutdown. It is. When ⁇ (50%) is over 135 ° C, shutdown response is poor when overheated due to poor shutdown characteristics when a polyolefin microporous membrane is used as a lithium battery separator.
- ⁇ Hm ( ⁇ 125 ° C) is a parameter that affects the molecular weight, degree of branching, and molecular entanglement! /, Degree of polyethylene.
- T (50%) is 135 ° C or less
- the shutdown temperature is low and the thermal shutdown shrinkage is within the temperature range up to the shutdown temperature.
- a microporous membrane having excellent properties can be obtained.
- ⁇ Hm ( ⁇ 125 ° C) is preferably 17% or less.
- a polyethylene resin sample [molded product melt-pressed at 210 ° C (thickness: 0.5 mm)] was statically placed in the sample holder of a scanning differential calorimeter (Perkin Elmer, Inc., Pyris Diamond DSC). Heat at 230 ° C for 1 minute in a nitrogen atmosphere, cool to 30 ° C in 10 ° CZ minutes, hold at 30 ° C for 1 minute, up to 230 ° C at a rate of 3-20 ° CZ Heated. The heating rate is preferably in the range of 5 to 15 ° CZmin, more preferably 10 ° CZmin. As shown in Fig. 1, the area S force of the region (shown by hatching) surrounded by the DSC curve (melting endothermic curve) and the baseline obtained during the heating process was also calculated. Calorific value (simple
- a Hm ( ⁇ 125 ° C) is the low-temperature region when the above region is divided by a straight line perpendicular to the base line at 125 ° C (the part indicated by hatching). )
- Area S is the low-temperature region when the above region is divided by a straight line perpendicular to the base line at 125 ° C (the part indicated by hatching).
- the polyethylene-based resin may be a single composition or a composition having two or more types of polyethylene strength. May be.
- the polyethylene-based resin is (a) ultrahigh molecular weight polyethylene, (b) polyethylene other than ultrahigh molecular weight polyethylene, or (c) a mixture (polyethylene composition) of ultrahigh molecular weight polyethylene and other polyethylene. preferable.
- the weight average molecular weight of polyethylene ⁇ (Mw) of not particularly limited, is preferably 1 X 10 4 to 1 X 10 7, Yori preferably 5 10 4-15 10 6 Deari Particularly preferred is 1 10 5 to 5 10 6 .
- Ultra high molecular weight polyethylene has a Mw of 7 ⁇ 10 5 or more.
- the ultrahigh molecular weight polyethylene may be not only an ethylene homopolymer but also an ethylene ⁇ a-olefin copolymer containing a small amount of other ⁇ -olefin.
- ⁇ -olefins other than ethylene propylene, butene-1, pentene-1, hexene-1, 4-methylpentene-1, otaten-1, butyl acetate, methyl methacrylate and styrene are preferable.
- Mw of ultra high molecular weight polyethylene is preferably 1 x 10 6 to 15 x 10 6, more preferably 1 x 10 6 to 5 x 10 6 .
- Polyethylenes other than ultra-high molecular weight polyethylene have a Mw of 1 x 10 4 or more and less than 7 x 10 5 , and high density polyethylene, medium density polyethylene, branched low density polyethylene and chained low density polyethylene are preferred. Polyethylene is more preferred. Polyethylene with an Mw force of 1 X 10 4 or more and less than 7 X 10 5 is not only a homopolymer of ethylene but also a co-polymer containing a small amount of other ⁇ -olefins such as propylene, butene-1, and hexene-1. Combined may be used. Such a copolymer is preferably produced using a single-site catalyst.
- the polyethylene other than the ultra high molecular weight polyethylene is not limited to a single product, and may be a mixture of two or more types of polyethylene other than the ultra high molecular weight polyethylene.
- Polyethylene yarn is composed of ultra high molecular weight polyethylene with an Mw force of 10 5 or more and other polyethylenes with an Mw of 1 X 10 4 or more and less than 7 X 10 5 (high density polyethylene, medium density polyethylene, branched low Density polyethylene and chain low density polyethylene force At least one kind).
- Ultra high molecular weight polyethylene and other polyethylenes may be the same as described above.
- This polyethylene yarn composition can easily control the molecular weight distribution [mass average molecular weight Z number average molecular weight (MwZMn)] according to the application.
- MwZMn mass average molecular weight
- the composition of the said ultra high molecular weight polyethylene and a high density polyethylene is preferable.
- the Mw of the high density polyethylene used in the polyethylene composition is preferably 1 x 10 5 or more and less than 7 x 10 5, 1 x 10 5 to 5 x 10 5 is more preferred 2 x 10 5 to 4 x 10 5 Most preferred.
- the content of the ultrahigh molecular weight polyethylene in the polyethylene composition is preferably 2 to 50% by mass, preferably 1% by mass or more, based on 100% by mass of the entire polyethylene composition.
- MwZMn is a measure of molecular weight distribution. The larger this value, the wider the molecular weight distribution.
- the MwZMn of the polyethylene-based resin is not limited, but when the polyethylene-based resin is composed of any of the above (a) to (c), 5 to 300 is preferable, and 10 to 100 is more preferable. If Mw / Mn is less than 5, the high molecular weight component is too much and melt extrusion is difficult, and if MwZMn is more than 300, the low molecular weight component is too much and the strength of the microporous membrane is reduced.
- MwZMn of polyethylene can be appropriately adjusted by multistage polymerization.
- the multi-stage polymerization method a two-stage polymerization in which a high molecular weight polymer component is generated in the first stage and a low molecular weight polymer component is generated in the second stage is preferable.
- the greater the MwZMn the greater the difference in Mw between ultrahigh molecular weight polyethylene and other polyethylenes, and vice versa.
- the MwZMn of the polyethylene yarn composite can be appropriately adjusted depending on the molecular weight and mixing ratio of each component.
- polyethylene-based resin examples include -Polonhard 6100A, 7300A, and 5110A (trade names, manufactured by Tosoh Corporation), Nozzetas 640UF, 780UF (trade names, manufactured by Prime Polymer Co., Ltd.), and the like.
- Polyolefin resin is a composition containing polyolefin resin other than polyethylene and resin other than polyolefin as long as the effect of the present invention is not impaired. It may be. Therefore, the term “polyolefin resin” should be understood to include not only polyolefin but also resins other than polyolefin.
- Polyolefins other than polyethylene include polypropylene, polybutene-1, polypentene-1, polyhexene-1, poly-4-methylpentene-1, polyoctene-1 with a Mw of 1 x 10 4 to 4 x 10 6 , Polyacetic acid butyl, polymethyl methacrylate, polystyrene and ethylene ' ⁇ -olefin copolymer, and a group strength that also has polyethylene wax strength of ⁇ w ⁇ X 10 3 to 1 X 10 4 It is necessary to use at least one selected it can.
- Polypropylene, polybutene-1, polypentene-1, polyhexene-1, poly 4-methylpentene-1, polyoctene-1, polybutyl acetate, polymethyl methacrylate and polystyrene are not only homopolymers but also other ⁇ It may be a copolymer containing -olefin.
- Examples of the resin other than polyolefin include heat-resistant resin having a melting point or glass transition temperature (Tg) of 150 ° C or higher.
- Tg melting point or glass transition temperature
- crystalline resin having a melting point of 150 ° C or higher including partially crystalline resin
- amorphous resin having a Tg of 150 ° C or higher are preferable.
- the melting point and Tg can be measured according to JIS K7121 (the same applies hereinafter).
- the meltdown temperature is further improved when the polyolefin microporous membrane is used as a battery separator, so that the high-temperature storage characteristics of the battery are improved.
- the upper limit of the melting point or Tg of the heat-resistant resin is not particularly limited, but is preferably 350 ° C. or less from the viewpoint of ease of kneading with the polyethylene resin.
- the melting point or Tg of the heat-resistant resin is more preferably 170 to 260 ° C.
- the heat-resistant resin include polyester [for example, polybutylene terephthalate (melting point: about 160 to 230 ° C), polyethylene terephthalate (melting point: about 250 to 270 ° C), etc.], fluorine resin, Polyamide (melting point: 215-265 ° C), polyarylene sulfide, isotactic polystyrene (melting point: 230 ° C), polyimide (Tg: 280 ° C or higher), polyamideimide (Tg: 280 ° C) ), Polyethersulfone (Tg: 223 ° C), Polyetheretherketone (melting point: 334 ° C), Polycarbonate (melting point: 220-240 ° C), Senorelose acetate (melting point: 220 ° C), Senorel roast Examples thereof include rear acetate (melting point: 300 ° C), polysulfone (Tg: 190 ° C), and polyetherimide (mel
- the heat-resistant resin is not limited to a single resin component, and may be a plurality of resin components.
- the addition amount of the heat-resistant resin is preferably 3 to 30% by mass, more preferably 5 to 25% by mass, with the total of the polyethylene-based resin and the heat-resistant resin being 100% by mass. preferable. If the content exceeds 30% by mass, the puncture strength, tensile rupture strength, and film smoothness are lowered.
- an inorganic filler may be added to the polyolefin resin.
- the inorganic filler include silica, alumina, silica alumina, zeolite, my strength, clay, kaolin, talc, calcium carbonate, calcium oxide, calcium sulfate, barium carbonate, barium sulfate, magnesium carbonate, magnesium sulfate, magnesium oxide, Examples include diatomaceous earth, glass powder, aluminum hydroxide, titanium dioxide, zinc oxide, satin white, and acid clay.
- Inorganic fillers may be used alone or in combination of two or more. Of these, silica and Z or calcium carbonate are preferably used.
- the addition amount of the inorganic filler is more preferably 0.5 to 3 parts by mass, preferably 0.1 to 5 parts by mass with respect to 100 parts by mass of the total amount of polyolefin resin and filler.
- the method for producing a polyolefin microporous membrane according to the present invention comprises: (1) a step of preparing a polyolefin resin solution by melting and kneading the polyolefin resin and a film forming solvent, and (2) the obtained polyolefin resin solution.
- a step of extruding from a die (3) a step of cooling the obtained extruded product to form a gel sheet, (4) a solvent removal step for film formation, and (5) a drying step. That is, it is produced by a so-called wet method.
- either (6) Stretching process,) Hot roll treatment process, (8) Hot solvent treatment process, or (9) Heat setting treatment process is provided between steps (3) and (4). May be.
- step (5) (10) step of stretching the microporous membrane, (11) heat treatment step, (12) cross-linking treatment step by ionizing radiation, (13) hydrophilization step, (14) surface coating step, etc. Can be provided. If it is produced by a dry method (a method of making it porous by stretching), it may be disadvantageous from the wet method in terms of the shutdown temperature.
- the polyolefin resin solution is prepared by adding a suitable film-forming solvent to the polyolefin resin and then melt-kneading.
- a suitable film-forming solvent for polyolefin resin solution, each of the above inorganic fillers, antioxidants, UV absorbers, anti-blocking agents, pigments, dyes, etc.
- a seed additive can be added as long as the effects of the present invention are not impaired.
- finely divided silicic acid can be added as a pore former.
- a liquid solvent and a solid solvent can be used.
- the liquid solvent include nonane, decane, decalin, paraxylene, undecane, dodecane, aliphatic hydrocarbons such as liquid paraffin, and mineral oil fractions having boiling points corresponding to these.
- a non-volatile liquid solvent such as liquid paraffin.
- the solid solvent preferably has a melting point of 80 ° C. or lower. Examples of such a solid solvent include paraffin wax, seryl alcohol, stearyl alcohol, and dicyclohexyl phthalate.
- a liquid solvent and a 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. If the viscosity at 25 ° C is less than 30 cSt, kneading and foaming are difficult. On the other hand, if it exceeds 500 cSt, it is difficult to remove the liquid solvent.
- the melt kneading method is not particularly limited, but a method of uniformly kneading in an extruder is preferable.
- the melt kneading temperature may be appropriately set depending on the components of the polyolefin resin, but is generally set to a melting point of 13 ⁇ 41 + 10 to 13 ⁇ 41 + 110 of the polyolefin resin.
- the melting point Tm of the polyolefin resin is the melting point when the polyolefin resin is (a) ultra-high molecular weight polyethylene, (b) other polyethylene, or (c) a polyethylene composition, and the polyolefin resin is other than polyethylene.
- the melting point of the ultrahigh molecular weight polyethylene, the other polyethylene, or the polyethylene composition containing the above composition (the same applies hereinafter).
- Ultra high molecular weight polyethylene, other polyethylenes, and polyethylene compositions have a melting point of about 130-140 ° C. Therefore, the melt kneading temperature is preferably 140 to 250 ° C, more preferably 170 to 240 ° C.
- the film-forming solvent may be added before the start of kneading, or during the kneading, an intermediate force of a twin screw extruder may be added, but the latter is preferred. It is preferable to add an antioxidant to prevent oxidation of the polyolefin resin during melt kneading.
- twin screw extruder As the extruder, a twin screw extruder is preferable.
- the twin screw extruder is a meshing type rotating in the same direction.
- a misalignment of a shaft extruder, a meshing type counter-rotating twin screw extruder, a non-meshing type co-rotating twin screw extruder and a non-meshing type counter-rotating twin screw extruder can be offset!
- a meshing type co-rotating twin screw extruder is preferred in that it has a self-cleaning action and can reduce the load and increase the number of rotations compared to the different direction rotating type.
- the screw length (L) to diameter (D) ratio (LZD) of the twin-screw extruder is preferably in the range of 20-100, more preferably in the range of 35-70.
- LZD is less than 20, melt kneading becomes insufficient. If the LZD exceeds 100, the residence time of the polyolefin resin solution increases too much.
- the shape of the screw is not particularly limited and may be a known one.
- the inner diameter of the twin screw extruder is preferably 40 to 100 mm.
- the ratio of the amount Q (kg / h) of polyolefin resin to the screw rotation speed Ns (rpm) is preferably set to 0.1 to 0.55 kgZhZim. . If QZNs is less than 0.1 kgZhZipm, the polyolefin resin will be excessively broken and the meltdown temperature will be lowered, and the film-breaking resistance against temperature rise after shutdown will deteriorate. On the other hand, when QZNs exceeds 0.55 kgZhZrpm, it cannot be uniformly kneaded.
- the ratio QZNs is more preferably 0.2 to 0.5 kgZhZ rpm.
- the screw rotation speed Ns is more preferably 250 rpm or more. The upper limit of the screw speed Ns is not particularly limited, but 500 rpm is preferable.
- the concentration of the resin in the polyolefin resin solution is 10 to 50% by mass, preferably 20 to 45% by mass, based on 100% by mass of the total of the polyolefin resin and the film-forming solvent. If the proportion of the polyolefin resin is less than 10% by mass, productivity is lowered, which is not preferable. When extruding the polyolefin resin solution, the swell and neck-in increase at the die outlet, and the moldability and self-supporting property of the extruded product deteriorate. On the other hand, if the proportion of the polyolefin resin exceeds 50% by mass, the moldability of the extruded product is lowered.
- the melt-kneaded polyolefin resin solution is extruded directly or via another extruder, or after cooling and pelletizing and extruding again through the extruder.
- a force using a sheet die having a generally rectangular base, a double cylindrical hollow die, an inflation die, and the like can also be used.
- the die gap is typically 0.1-5mm When extruding, heat to 140-250 ° C.
- the extrusion rate of the heated solution is preferably 0.2 to 15 m / min.
- a gel-like sheet is formed by cooling the extruded compact. Cooling is preferably performed at a speed of at least 50 ° CZ to at least the gel temperature. By performing such cooling, a structure in which the polyolefin resin phase is microscopically separated by a film forming solvent (a gel structure comprising a polyolefin resin phase and a film forming solvent phase) can be fixed. Cooling is preferably performed to 25 ° C or less. In general, when the cooling rate is slowed down, the pseudo cell unit becomes large and the higher order structure of the resulting gel-like sheet becomes rough, but when the cooling rate is fast, it becomes a dense cell unit.
- a method using a cooling roll which can use a method of contacting with a cooling medium such as cold air or cooling water, a method of contacting with a cooling roll, or the like is preferable.
- the temperature of the chill roll is preferably the crystallization temperature of the polyolefin resin Tc—120 ° C or higher to Tc—5 ° C or lower, preferably Tc—115 ° C or higher to Tc—15 ° C or lower. Is more preferable. If the temperature of the chill roll exceeds Tc 5 ° C, sufficient rapid cooling cannot be achieved.
- the crystallization temperature Tc of the polyolefin resin is the crystallization temperature when the polyolefin resin is the above (a) ultrahigh molecular weight polyethylene, (b) polyethylene other than ultrahigh molecular weight polyethylene, or (c) polyethylene composition.
- the crystallization temperature of the ultrahigh molecular weight polyethylene, the other polyethylene, or the polyethylene composition that includes the above composition is a value determined by JIS K7121.
- the crystallization temperature of ultrahigh molecular weight polyethylene, other polyethylenes and polyethylene compositions is generally 110-115 ° C. Therefore, the temperature of the cooling roll should be in the range of -10 to 105 ° C, and preferably in the range of 5 to 95 ° C.
- the contact time between the cooling roll and the sheet is preferably 1 to 30 seconds, more preferably 2 to 15 seconds.
- a cleaning solvent is used to remove (wash) the liquid solvent.
- the removal (washing) of the liquid solvent can be performed using a known washing solvent.
- the cleaning solvent include saturated hydrocarbons such as pentane, hexane and heptane, chlorinated hydrocarbons such as methylene chloride and carbon tetrachloride, ethers such as jetyl ether and dioxane, and ketones such as methyl ethyl ketone. , Fluorocarbon chain such as trifluoride tan, CF, CF
- Bonbons, CHF, etc. cyclic hide mouth fluorocarbon, CFOCH, CFOCH, etc.
- Examples include emissive solvents. These cleaning solvents have a low surface tension (eg, 24 mN / m or less at 25 ° C). By using a low surface tension cleaning solvent, the network that forms micropores is prevented from shrinking due to the surface tension of the gas-liquid interface during drying after cleaning, and has a high porosity and permeability. A microporous membrane is obtained.
- the membrane can be cleaned by a method of immersing in a cleaning solvent, a method of showering the cleaning solvent, or a combination thereof.
- the washing solvent is preferably used in an amount of 300 to 30,000 parts by mass with respect to 100 parts by mass of the film before washing.
- the washing with the washing solvent is preferably performed until the residual amount of the liquid solvent is less than 1% by mass of the initial amount of the added salt.
- the polyolefin microporous film obtained by removing the film forming solvent is dried by a heat drying method, an air drying method or the like.
- the drying temperature is preferably below the crystal dispersion temperature Ted of the polyolefin resin, especially at least 5 ° C lower than Ted! /.
- the crystal dispersion temperature Ted of the polyolefin resin is such that when the polyolefin resin is the above-mentioned (a) ultra-high molecular weight polyethylene, (b) polyethylene other than ultra-high molecular weight polyethylene, or (c) a polyethylene composition.
- the polyolefin resin is a composition containing polyolefin other than polyethylene or a heat-resistant resin
- the above composition is included among ultrahigh molecular weight polyethylene, other polyethylene, or polyethylene composition.
- the crystal dispersion temperature is a value obtained by measuring the temperature characteristic of dynamic viscoelasticity based on ASTM D 4065.
- the above ultra-high molecular weight polyethylene, polyethylene other than ultra-high molecular weight polyethylene, and polyethylene yarns have a crystal dispersion temperature of about 90-100 ° C.
- the drying is more preferably performed until the residual porous solvent becomes 5% by mass or less, with the microporous membrane being 100% by mass (dry weight), and more preferably 3% by mass or less. Insufficient drying is preferable because the porosity of the microporous membrane decreases and the permeability deteriorates when heat treatment is performed later.
- the gel-like sheet is preferably stretched at a predetermined ratio after heating by a tenter method, a roll method, an inflation method, a rolling method, or a combination of these methods. Since the gel-like sheet contains a film-forming solvent, it can be stretched uniformly. The stretching improves the mechanical strength and enlarges the pores, so that it is particularly preferable when used as a battery separator.
- the stretching may be uniaxial stretching or biaxial stretching, but biaxial stretching is preferred. In the case of biaxial stretching, any of simultaneous biaxial stretching, sequential stretching or multi-stage stretching (for example, simultaneous biaxial stretching and sequential stretching yarn combination) may be used, but simultaneous biaxial stretching is particularly preferable.
- the draw ratio is preferably 2 times or more, more preferably 3 to 30 times.
- biaxial stretching it is preferable that at least 3 times in any direction and 9 times or more in area magnification. If the area magnification is less than 9 times, stretching is insufficient and a microporous membrane with high elasticity and high strength cannot be obtained. On the other hand, if the area magnification exceeds 400 times, there will be restrictions in terms of stretching equipment and stretching operations. The upper limit of area magnification is 50 times.
- the stretching temperature is more preferably within the range of the above-mentioned crystal dispersion temperature Ted to less than the above melting point Tm, which is preferably the melting point Tm + 10 ° C or less of the polyolefin resin.
- Tm melting point
- Tm + 10 ° C melting point
- the polyethylene-based resin melts and molecular chains cannot be oriented by stretching.
- Ted softness of the polyethylene-based resin
- the film does not break due to stretching and cannot be stretched immediately at high magnification.
- the polyethylene-based resin has a crystal dispersion temperature of about 90 to 100 ° C. Therefore, the stretching temperature is usually in the range of 90 to 140 ° C, preferably in the range of 100 to 130 ° C.
- the stretching speed is preferably 1 to 80% Z seconds in the stretching axis direction.
- the length is set to 1 to 80% Z seconds in the longitudinal direction (MD direction) or the transverse direction (TD direction).
- TD direction transverse direction
- it should be 1 to 80% Z seconds in the MD and TD directions.
- the stretching speed (% z seconds) represents the ratio of the length stretched per second with the length in the stretching axis direction before stretching as 100% at the portion where the gel sheet is stretched. This stretching speed
- the stretching speed is more than 80% Z seconds, the heat shrinkage is reduced.
- the stretching speed is more preferably 2 to 70% Z seconds. In the case of biaxial stretching, as long as each stretching speed in the MD direction and TD direction is 1 to 80% Z seconds, the MD direction and T
- a temperature distribution may be provided in the film thickness direction and the film may be stretched to obtain a microporous film having excellent single-layer mechanical strength.
- the method is disclosed in Japanese Patent No. 334.
- the heat resistance may be applied to at least one surface of the gel sheet to improve the compression resistance of the microporous membrane.
- Japanese Patent Application 2005-2710 Japanese Patent Application 2005-2710
- a treatment for bringing the gel-like sheet into contact with a hot solvent may be performed, whereby a microporous film having further excellent mechanical strength and permeability can be obtained.
- the method is disclosed in WO 2000/2.
- the stretched gel sheet may be heat set.
- the specific method is disclosed in, for example,
- the polyolefin microporous membrane after drying may be stretched in at least a uniaxial direction within a range not impairing the effects of the present invention. This stretching can be performed by the tenter method or the like as described above while heating the film.
- the temperature at which the microporous membrane is stretched is preferably below the melting point Tm of the polyolefin resin. More preferably, it is within the range of ⁇ Tm or less. Specifically, it is in the range of 90 to 135 ° C, preferably in the range of 95 to 130 ° C.
- biaxial stretching it is preferably 1.1 to 2.5 times at least in the uniaxial direction, more preferably 1.1 to 2.0 times. If this magnification is over 2.5 times, the shutdown temperature may be adversely affected.
- the dried film it is preferable to subject the dried film to heat setting and Z or heat relaxation treatment by a known method LV. These may be appropriately selected according to the physical properties required for the polyolefin microporous membrane.
- the crystal is stabilized by the heat treatment, and the lamellar layer is made uniform. In particular, it is preferable to heat relax after stretching the microporous membrane.
- the polyolefin microporous membrane after drying may be subjected to crosslinking treatment by irradiation with ionizing radiation such as ⁇ -ray, j8-ray, ⁇ -ray and electron beam.
- ionizing radiation such as ⁇ -ray, j8-ray, ⁇ -ray and electron beam.
- electron beam irradiation an acceleration voltage of 100 to 300 kV is preferred, with an electron dose of 0.1 to 100 Mrad being preferred.
- the meltdown temperature of the microporous membrane rises due to the crosslinking treatment.
- the dried polyolefin microporous membrane may be hydrophilized by performing a monomer graft treatment, a surfactant treatment, a corona discharge treatment, a plasma treatment or the like by a known method.
- the polyolefin microporous membrane is formed by coating the surface with a fluororesin porous material such as polyvinylidene fluoride or polytetrafluoroethylene, or a porous material such as polyimide or polyphenylene sulfide.
- a fluororesin porous material such as polyvinylidene fluoride or polytetrafluoroethylene
- a porous material such as polyimide or polyphenylene sulfide.
- a coating layer containing polypropylene may be formed on at least one surface of the dried polyolefin microporous membrane. Examples of the covering polypropylene include those disclosed in WO2005-054350.
- the polyolefin microporous membrane has the following physical properties.
- Air permeability change rate of 1 X 10 4 sec / 100 cm 3 Z ° C or higher Air permeability change rate after shutdown is 1 X 10 4 sec / 100 cm 3 Z ° C or higher.
- Air permeability change rate is less than 1 ⁇ 10 4 sec / 100 cm 3 / ° C, when the polyolefin microporous membrane is used as a lithium battery separator, the shutoff response during overheating is low.
- the air permeability change rate is preferably 12,000 sec / 100 cm 3 Z ° C or higher.
- the polyolefin microporous membrane according to the preferred embodiment of the present invention has the following physical properties.
- the air permeability in terms of the film thickness is 20 to 800 sec / 100 cm 3
- the battery has a large battery capacity and good cycle characteristics. If the air permeability is less than 20 sec / 100 cm 3 , the battery will not shut down sufficiently when the temperature inside the battery rises.
- the porosity is less than 25%, good air permeability cannot be obtained. On the other hand, if it exceeds 80%, the strength when the polyolefin microporous membrane is used as a battery separator is insufficient, and there is a great risk that the electrode is short-circuited.
- the puncture strength is less than 4,000 ⁇ 20 / ⁇ ⁇ , the short circuit of the electrode may occur when the polyolefin microporous membrane is incorporated in a battery as a battery separator.
- the puncture strength is preferably 4,500 mN / 20 ⁇ m or more.
- shutoff response during overheating is low.
- the polyolefin microporous membrane according to a preferred embodiment of the present invention has a balance between the shutdown characteristics, the thermal start shrinkage in the temperature range up to the shutdown temperature, and the meltdown characteristics. Excellent as well as permeability and mechanical properties.
- the separator for a battery comprising the polyolefin microporous membrane of the present invention preferably has a film thickness of 7 to 35 / ⁇ ⁇ , preferably having a force of 5 to 50 m, which can be appropriately selected depending on the type of battery. More preferably.
- the polyolefin microporous membrane of the present invention is preferably used as a separator for secondary batteries such as nickel-hydrogen batteries, nickel-cadmium batteries, nickel zinc batteries, silver zinc batteries, lithium secondary batteries, lithium polymer secondary batteries and the like. Force that can be used It is particularly preferable to use as a separator of a lithium secondary battery.
- a lithium secondary battery will be described as an example.
- a positive electrode and a negative electrode are laminated via a separator, and the separator contains an electrolytic solution (electrolyte).
- the structure of the electrode is not particularly limited, and is a known structure. Good.
- an electrode structure in which disc-shaped positive and negative electrodes are arranged to face each other coin type
- an electrode structure in which flat plate-like positive and negative electrodes are alternately stacked laminated type
- strip-shaped positive and negative electrodes It is possible to make an electrode structure (winding type) or the like that is wound by overlapping.
- the positive electrode usually has (a) a current collector and (b) a layer formed on the surface thereof and containing a positive electrode active material capable of occluding and releasing lithium ions.
- the positive electrode active material include transition metal oxides, composite oxides of lithium and transition metals (lithium composite oxides), and inorganic compounds such as transition metal sulfides. Transition metals include V, Mn, Fe, Co, Ni etc. are mentioned.
- Preferable examples of the lithium composite oxide include lithium nickelate, lithium conoleate, lithium manganate, and a layered lithium composite oxide based on an ⁇ -NaFeO type structure.
- the negative electrode has (a) a current collector and (b) a layer formed on the surface thereof and containing a negative electrode active material.
- the negative electrode active material include carbonaceous materials such as natural graphite, artificial graphite, coatas, and carbon black.
- the electrolytic solution is obtained by dissolving a lithium salt in an organic solvent.
- Lithium salts include LiCIO, LiPF, LiAsF, LiSbF, LiBF, LiCF SO, LiN (CF SO), LiC (CF SO), Li
- LiAlCl LiAlCl and the like. These may be used alone or as a mixture of two or more.
- the organic solvent examples include organic solvents having a high boiling point and a high dielectric constant such as ethylene carbonate, propylene carbonate, ethyl methyl carbonate, and ⁇ -petit-mouth rataton, tetrahydrofuran, 2-methyltetrahydrofuran, dimethoxyethane, dioxolane, dimethyl, and the like.
- examples thereof include low boiling point and low viscosity organic solvents such as carbonate and jetyl carbonate. These may be used singly or as a mixture of two or more.
- a high dielectric constant organic solvent has a high viscosity
- a low viscosity organic solvent has a low dielectric constant. Therefore, it is preferable to use a mixture of both.
- the separator When the battery is assembled, the separator is impregnated with the electrolytic solution. Thereby, ion permeability can be imparted to the separator (polyolefin microporous membrane).
- the impregnation treatment is performed by immersing a polyolefin microporous membrane in an electrolyte at room temperature.
- a positive electrode sheet, a separator made of a polyolefin microporous membrane, and a negative electrode sheet are laminated in this order, and the obtained laminate is wound from one end to form a wound electrode element.
- the obtained electrode element is inserted into a battery can, impregnated with the above electrolyte, and a battery lid serving as a positive electrode terminal provided with a safety valve is also clamped via a gasket to produce a battery.
- UHMWPE ultrahigh molecular weight polyethylene
- HDPE high density polyethylene
- PE weight average molecular weight polyethylene
- a Hm ( ⁇ 125 ° C) measured for PE composition consisting of UHMWPE and HDPE is 14%
- T (50%) is 132.5 ° C
- melting point is 135 ° C
- crystal dispersion temperature is 100 ° C.
- Mw of UHMWPE and HDPE is gel permeation chromatography under the following conditions.
- Calibration curve Prepared from a calibration curve obtained using a monodisperse polystyrene standard sample using a predetermined conversion constant.
- the obtained polyethylene solution was also fed to a T-die with a twin-screw extruder force, and extruded so as to form a sheet-like molded product having a thickness of mm.
- the extruded molded body was cooled while being drawn with a cooling roll adjusted to 50 ° C. to form a gel-like sheet.
- the obtained gel-like sheet was simultaneously biaxially stretched at a temperature of 20% Z seconds in both directions so as to be 5 times in both the MD direction and the TD direction at 114 ° C by a patch type stretching machine.
- the stretched gel-like sheet is fixed to a frame plate [size: 30 cm x 30 cm, made of aluminum], immersed in a methylene chloride washing bath adjusted to 25 ° C, and rocked at 100 rpm for 3 minutes. Washed to remove 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 polyethylene microporous membrane.
- the liquid paraffin removing step was performed in the same manner as in Example 1, and a cleaning film was prepared and dried.
- the obtained film was stretched again at a temperature of 126 ° C to 1.1 times in the TD direction, heat relaxed at 126 ° C until it contracted to the size before re-stretching, and heat fixed at that temperature for 10 minutes
- a polyethylene microporous membrane was produced in the same manner as in Example 1 except for the treatment.
- Mw of 2.2 X 10 UHMWPE30 mass 0/0, HDPE40 mass 0/0 Mw of 3.0 X 10 5 of 6, and Mw is low molecular weight polyethylene 30 wt% force 2.0 X 10 3
- a Hm ( ⁇ 125 ° C ) Is 26%, T (50%) is a polyethylene thread and composition of 133.6 ° C, and the heat setting temperature is set to 118 ° C.
- Mw is UHMWPE20 mass 0/0 2.5 X 10 6
- a Hm ( ⁇ 125 ° C) is 28%
- T (50%) is 133.1
- a polyethylene microporous membrane was prepared in the same manner as in Example 1 except that a polyethylene composition at ° C was used, the stretching temperature was set to 108 ° C, and the heat setting treatment temperature was set to 118 ° C.
- UHMWPE20 mass Mw of 2.5 X 10 6 0/0, and HDPE80 mass Mw of 3.0 X 10 5 0/0 Tona is, in A Hm ( ⁇ 125 ° C) is 24%, T (50%) is 133.5
- a polyethylene microporous membrane was prepared in the same manner as in Example 1 except that a polyethylene composition at ° C was used, the stretching rate was 100%, and the heat setting treatment temperature was 120 ° C.
- Mw is UHMWPE20 mass 0/0
- Mw of 2.5 X 10 6 consists HDPE80 mass 0/0 of 3.0 X 10 5
- ⁇ Hm ( ⁇ 125 ° C) is at 21%
- T (50%) is 132.2 ° C
- a polyethylene solution was prepared in the same manner as in Example 1, except that the ratio of the amount Q of the polyethylene composition charged into the extruder with respect to the screw rotation number Ns was 0.075.
- a polyethylene microporous membrane was prepared in the same manner as in Example 1 except that the obtained polyethylene solution was used and the heat setting treatment temperature was 120 ° C.
- a polyethylene solution was prepared in the same manner as in Comparative Example 5 except that the ratio of the amount Q of the polyethylene composition charged into the extruder with respect to the screw rotation speed Ns was 0.6, but a uniform kneaded product was not obtained.
- the film thickness was measured with a contact thickness meter over a 30 cm width of the microporous membrane at a longitudinal interval of 5 mm, and the measured thickness values were averaged.
- a microporous membrane with a thickness of T is 2 mm.
- Measurement was performed by ASTM D882 using a strip-shaped test piece having a width of 10 mm.
- the shutdown temperature (T) is 5% for polyethylene microporous membrane.
- EGO-1T Oken type air permeability meter
- the temperature at the four SD points was determined and used as the shutdown start temperature ( ⁇ ).
- thermomechanical analyzer TMAZSS6000, manufactured by Seiko Instruments Inc.
- TD 10 mm
- MD X 3 mm
- the temperature was raised from room temperature, and the dimensional change rate at 130 ° C was measured three times based on the dimensions at 23 ° C, and the average value was calculated.
- meltdown temperature (T) After reaching the above shutdown temperature, heating was further continued at a rate of 5 ° CZmin, and the temperature at which the air permeability again became 1 ⁇ 10 5 sec / 100 cm 3 was determined and used as the meltdown temperature (T).
- Example No. Example 1 Example 2
- Example 3 Example 4 Resin composition
- PE concentration (mass%) 25 25 25 25 25 ⁇ Condition Q (* (kg / h) 120 120 120 120 120 120 120 120
- Ns represents the screw speed
- the polyethylene microporous membranes of Examples 1 to 4 have a shutdown start temperature of 130 ° C or lower, a shutdown speed of 10,000 sec / 100 cm 3 Z ° C or higher, and 130 ° C.
- the shrinkage ratio is 20% or less
- the shutdown temperature is 135 ° C or less
- the meltdown temperature is 150 ° C or more, and it has excellent heat shrinkage, shutdown characteristics, and meltdown characteristics. I understand. Furthermore, the permeability and mechanical strength were also excellent.
- the shutdown start temperature and the shutdown temperature are higher than those of Examples 1 to 4, and the shutdown speed is 8,000 s. ec / 100 cm 3 It was inferior at less than Z ° C.
- the films of Comparative Examples 2 to 4 have A Hm ( ⁇ 125 ° C) of more than 20%, and in particular, the film of Comparative Example 4 has a stretching speed of more than 80% Z seconds. Compared with heat shrinkage, it was inferior.
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Abstract
Description
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Priority Applications (6)
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CN200680043696XA CN101313016B (zh) | 2005-11-24 | 2006-11-22 | 聚烯烃微多孔膜及其制造方法、以及电池用隔离件和电池 |
JP2007546469A JP5250263B2 (ja) | 2005-11-24 | 2006-11-22 | ポリオレフィン微多孔膜及びその製造方法、並びに電池用セパレータ及び電池 |
KR1020087013387A KR101340394B1 (ko) | 2005-11-24 | 2006-11-22 | 폴리올레핀 미세 다공막 및 그 제조 방법, 및 전지용세퍼레이터 및 전지 |
US12/094,909 US20090042008A1 (en) | 2005-11-24 | 2006-11-22 | Microporous polyolefin membrane, its production method, battery separator and battery |
CA2630800A CA2630800C (en) | 2005-11-24 | 2006-11-22 | Microporous polyolefin membrane, its production method, battery separator and battery |
EP20060833139 EP1956040B1 (en) | 2005-11-24 | 2006-11-22 | Microporous polyolefin membrane, process for producing the same, separator for cell, and cell |
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JP5296917B1 (ja) * | 2012-11-16 | 2013-09-25 | 東レバッテリーセパレータフィルム株式会社 | 電池用セパレータ |
KR101378051B1 (ko) | 2012-11-16 | 2014-03-27 | 도레이 배터리 세퍼레이터 필름 주식회사 | 전지용 세퍼레이터 |
WO2014076994A1 (ja) | 2012-11-16 | 2014-05-22 | 東レバッテリーセパレータフィルム株式会社 | 電池用セパレータ |
WO2014126079A1 (ja) | 2013-02-13 | 2014-08-21 | 東レバッテリーセパレータフィルム株式会社 | 電池用セパレータ及びその電池用セパレータの製造方法 |
WO2015029944A1 (ja) | 2013-08-30 | 2015-03-05 | 東レバッテリーセパレータフィルム株式会社 | 電池用セパレータ及びその製造方法 |
JP5495457B1 (ja) * | 2013-08-30 | 2014-05-21 | 東レバッテリーセパレータフィルム株式会社 | 電池用セパレータ及びその電池用セパレータの製造方法 |
JP2015049961A (ja) * | 2013-08-30 | 2015-03-16 | 東レバッテリーセパレータフィルム株式会社 | 電池用セパレータ及びその電池用セパレータの製造方法 |
KR20150045407A (ko) | 2013-08-30 | 2015-04-28 | 도레이 배터리 세퍼레이터 필름 주식회사 | 전지용 세퍼레이터 및 그 제조 방법 |
WO2016024548A1 (ja) * | 2014-08-12 | 2016-02-18 | 東レバッテリーセパレータフィルム株式会社 | ポリオレフィン製微多孔膜およびその製造方法、非水電解液系二次電池用セパレータ、ならびに非水電解液系二次電池 |
KR20170041195A (ko) * | 2014-08-12 | 2017-04-14 | 도레이 배터리 세퍼레이터 필름 주식회사 | 폴리올레핀제 미세 다공막 및 이의 제조 방법, 비수 전해액계 이차전지용 세퍼레이터, 및 비수 전해액계 이차전지 |
US10658640B2 (en) | 2014-08-12 | 2020-05-19 | Toray Industries, Inc. | Polyolefin microporous membrane, production method thereof, separator for non-aqueous electrolyte secondary battery, and non-aqueous electrolyte secondary battery |
KR102344220B1 (ko) * | 2014-08-12 | 2021-12-27 | 도레이 카부시키가이샤 | 폴리올레핀제 미세 다공막 및 이의 제조 방법, 비수 전해액계 이차전지용 세퍼레이터, 및 비수 전해액계 이차전지 |
WO2017170289A1 (ja) * | 2016-03-31 | 2017-10-05 | 東レ株式会社 | ポリオレフィン微多孔膜及びその製造方法、電池用セパレータ並びに電池 |
Also Published As
Publication number | Publication date |
---|---|
CN101313016B (zh) | 2011-09-28 |
US20090042008A1 (en) | 2009-02-12 |
KR20080077972A (ko) | 2008-08-26 |
EP1956040A4 (en) | 2010-05-05 |
CA2630800C (en) | 2014-01-28 |
RU2411259C2 (ru) | 2011-02-10 |
RU2008125434A (ru) | 2009-12-27 |
TW200734177A (en) | 2007-09-16 |
EP1956040B1 (en) | 2012-01-04 |
TWI444296B (zh) | 2014-07-11 |
JP5250263B2 (ja) | 2013-07-31 |
CA2630800A1 (en) | 2007-05-31 |
KR101340394B1 (ko) | 2013-12-11 |
EP1956040A1 (en) | 2008-08-13 |
CN101313016A (zh) | 2008-11-26 |
JPWO2007060991A1 (ja) | 2009-05-07 |
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