JP5636618B2 - Composite porous membrane and method for producing the same - Google Patents

Description

  The present invention relates to a composite porous membrane in which a porous membrane containing a specific polyamide resin is laminated on a porous membrane made of a polyolefin resin. In particular, the present invention relates to a composite porous membrane useful as a separator for a lithium ion secondary battery, which is excellent in ion permeability and excellent in adhesion between a polyolefin-based porous membrane and a polyamide resin membrane.

  A porous membrane made of a thermoplastic resin is widely used as a material for separating, selectively permeating and isolating substances. For example, battery separators used in lithium ion secondary batteries, nickel-hydrogen batteries, nickel-cadmium batteries, polymer batteries, separators for electric double layer capacitors, reverse osmosis filtration membranes, ultrafiltration membranes, microfiltration membranes, etc. It is used in filters, moisture-permeable and waterproof clothing, medical materials, etc. In particular, polyethylene porous membranes are preferably used as separators for lithium ion secondary batteries because of their excellent electrical insulation properties and ion permeability due to electrolyte impregnation, and are resistant to electrolytes and acids. This is because it has not only a feature that it is excellent in chemical conversion property but also a hole closing effect that cuts off current at a temperature of about 120 to 150 ° C. at the time of abnormal battery temperature rise and suppresses excessive temperature rise. However, if the temperature continues to rise even after the pores are closed for some reason, a film breakage may occur at a certain temperature due to a decrease in viscosity of the melted polyethylene constituting the film and a contraction of the film. Also, if left at a constant high temperature, there is a possibility that a film breakage may occur after a certain period of time due to a decrease in viscosity of the melted polyethylene and a contraction of the film. This phenomenon is not limited to polyethylene, and even when other thermoplastic resins are used, the phenomenon cannot be avoided beyond the melting point of the resin constituting the porous film.

  In particular, lithium-ion battery separators are deeply involved in battery characteristics, battery productivity, and battery safety. Excellent mechanical characteristics, heat resistance, permeability, dimensional stability, pore clogging characteristics (shutdown characteristics), melting damage Film prevention characteristics (meltdown prevention characteristics) are required. Therefore, various heat resistance improvement studies have been made so far. Furthermore, in order to increase the battery capacity, it is predicted that further thinning will progress in order to increase not only the electrodes but also the area that can be filled in the container not only in the separator. As the porous film becomes thinner, it tends to be deformed in the plane direction, so the heat-resistant resin layer may peel off during processing of the composite porous film, in the slit process, or in the battery assembly process, ensuring safety. It becomes difficult.

  Moreover, in order to cope with cost reduction, it is expected that the battery assembly process will increase in speed. Therefore, the present inventors are required to have less trouble such as peeling of the heat-resistant resin layer even in such high-speed processing, and for that purpose, it is speculated that higher adhesion is required. .

  Patent Document 1 exemplifies a composite porous film obtained by applying a polyamide resin to a polyolefin-based porous film having a thickness of 25 μm. As in the case of Patent Document 1, when a polyamide resin is directly applied to a polyolefin-based porous membrane, the penetration of the resin component into the polyolefin-based porous membrane is inevitable, resulting in a significant increase in air resistance and pore blockage. A decline in functionality is inevitable. In such a method, in particular, when the thickness of the polyolefin-based porous film is as thin as less than 10 μm, the resin component easily fills the inside of the porous material, causing an extreme increase in air resistance. In addition, such a method also has a problem that the film thickness unevenness of the polyolefin-based porous film is likely to be related to the film thickness unevenness of the heat resistant resin layer, and the air resistance resistance is likely to vary.

  Patent Document 2 exemplifies an electrolyte-supported polymer film obtained by immersing and drying a nonwoven fabric made of aramid fibers having an average thickness of 36 μm in a dope containing a vinylidene fluoride copolymer that is a heat-resistant resin.

  In Patent Document 3, a composite porous membrane obtained by immersing a polypropylene porous membrane having a film thickness of 25.6 μm in a dope mainly composed of polyvinylidene fluoride, which is a heat-resistant resin, and undergoing solidification, washing, and drying processes. Is illustrated.

  When a non-woven fabric made of aramid fibers is immersed in a heat-resistant resin solution as in Patent Document 2, a heat-resistant porous layer is formed on the inside and both surfaces of the non-woven fabric, so that the communication holes inside the non-woven fabric are mostly covered. In other words, a significant increase in the air permeability resistance cannot be avoided, and a hole closing function that determines the safety of the separator cannot be obtained. Moreover, since it is difficult to reduce the thickness of a nonwoven fabric as compared to a polyolefin-based porous membrane, it is not suitable for increasing the capacity of a battery that will progress in the future.

  In Patent Document 3, the heat resistant porous layer is still formed on the inside and both surfaces of the polypropylene porous membrane, and a significant increase in the air permeability resistance cannot be avoided as in Patent Document 2, It is difficult to obtain an occlusion function.

  Thus, in a composite porous membrane in which a heat-resistant resin layer is laminated on a polyolefin-based porous membrane serving as a base film, the heat-resistant resin is infiltrated into the porous film serving as a base material. If the adhesion is improved, the increase in the air resistance increases, and if the penetration of the heat resistant resin is reduced, the increase in the air resistance can be suppressed, but the adhesion of the heat resistant resin layer is reduced. In particular, as separators become thinner, it is difficult to ensure safety, which is becoming more and more demanding, in view of speeding up in the battery assembly process. As described above, there has never been a composite porous film in which both the adhesiveness of the heat-resistant resin layer and the increase in air permeability resistance are compatible. Furthermore, if the thickness of the polyolefin-based porous film as the base material becomes thinner, it becomes more difficult to achieve both the adhesion of the heat-resistant resin layer and the increase in air resistance.

JP 2005-314635 A JP 2001-266842 A JP 2003-171495 A

  The present invention provides a composite porous membrane that achieves both excellent adhesion to a heat-resistant resin layer and a small increase in air resistance even when battery separators are made thinner in the future. The present invention aims to provide a battery separator particularly suitable for a lithium ion battery separator, which is suitable for increasing the capacity of the battery, excellent ion permeability, and high-speed processability in the battery assembly process.

The present invention has the following configurations (1) to (7).
(1) A composite porous membrane used as a battery separator, wherein a porous membrane A made of a polyolefin resin is laminated with a porous membrane B containing a polyamide resin containing an isophorone structure as an amine component The composite porous membrane is characterized in that the porous membrane satisfies the following formulas (A) to (F).
Thickness of porous membrane A <10 μm Formula (A)
0.01 μm ≦ average pore diameter of porous membrane A ≦ 0.3 μm Formula (B)
30% ≦ Porosity of porous membrane A ≦ 70% Formula (C)
Total thickness of composite porous membrane ≦ 13 μm Formula (D)
Peel strength at the interface between porous membrane A and porous membrane B ≧ 1.0 N / 25 mm
... Formula (E)
20 ≦ Y−X ≦ 100 Formula (F)
(X is the air resistance of the porous membrane A (second / 100 cc Air), Y is the air resistance of the entire composite porous membrane (second / 100 cc Air))
(2) The composite porous membrane according to (1), wherein the polyamide resin contains an isophorone structure in a proportion of 10 to 100 mol% with respect to the amine component.
(3) The composite porous membrane according to (1) or (2), wherein the air permeability resistance of the composite porous membrane is 50 to 600 seconds / 100 cc Air.
(4) The method for producing a composite porous membrane according to any one of (1) to (3), comprising the following steps (i) and (ii):
Step (i): After applying the polyamide resin solution on the base film, it is passed through a low humidity zone having an absolute humidity of less than 6 g / m ³ , and then high humidity having an absolute humidity of 6 g / m ³ or more and 25 g / m ³ or less. A step of forming a polyamide resin film on the base film through the zone, and a step (ii): the polyamide resin film formed in the step (i) and the porous film A made of a polyolefin-based resin are bonded together Then, a step of immersing in a coagulation bath to convert the polyamide resin film into a porous film B, washing and drying to obtain a composite porous film.
(5) The method for producing a composite porous membrane according to (4), wherein the substrate film is peeled after obtaining the composite porous membrane in step (ii).
(6) The method for producing a composite porous membrane according to (4) or (5), wherein the base film is a polyester film or a polyolefin film having a thickness of 25 to 100 μm.
(7) In the step (i), the passage time in the low humidity zone is 3 seconds or more and 20 seconds or less, and the passage time in the high humidity zone is 3 seconds or more and 10 seconds or less (4) to (6) The method for producing a composite porous membrane according to any one of the above.

  The composite porous membrane of the present invention has both excellent adhesion of the polyamide resin layer and a small increase in the air resistance, so that the battery has a high capacity, excellent ion permeability, and a battery assembly process. It is suitable for high-speed processability, and can be suitably used particularly for battery separators.

  The composite porous membrane of the present invention is obtained by laminating a porous membrane A made of a polyolefin resin and a porous membrane B containing a polyamide resin containing an isophorone structure as an amine component. Excellent adhesion of the polyamide resin layer is achieved without causing a significant increase in the air resistance.

  Here, the significant increase in the air resistance is that the difference between the air resistance (X) of the porous membrane A serving as the base material membrane and the air resistance (Y) of the composite porous membrane is 100 seconds / 100 cc Air. It means exceeding. The excellent adhesion of the polyamide resin layer means that the peel strength is 1.0 N / 25 mm or more, preferably 1.5 N / 25 mm or more, more preferably 2.0 N / 25 mm or more. If it is less than 1.0 N / 25 mm, the polyamide resin layer may be peeled off during high-speed processing in the battery assembly process. There is no particular upper limit on the peel strength, but 3.0 N / 25 mm is sufficient as adhesion.

First, the porous membrane A used in the present invention will be described.
As the resin constituting the porous membrane A, polyolefin resin is used, and polyethylene resin is particularly preferable. This is because, in addition to basic characteristics such as electrical insulation and ion permeability, it has a hole closing effect that cuts off the current and suppresses excessive temperature rise at abnormal battery temperature rise.

  Furthermore, the polyolefin-based resin constituting the porous membrane A has process workability and mechanical strength that can withstand various external pressures generated during winding with the electrode, such as tensile strength, elastic modulus, elongation, and piercing strength. The mass average molecular weight is preferably 300,000 or more, more preferably 400,000 or more, and most preferably 500,000 or more. In addition, when using these polyolefin-type resin, it is preferable that the polyolefin component which has the mass mean molecular weight of the said range contains 50 weight% or more, More preferably, it contains 60 weight% or more. When the content is lower than the above range, the melt viscosity is low, so the mechanical properties are significantly reduced when the temperature is raised above the pore closing temperature. Melt film breakage may occur.

  The phase structure of the porous membrane A varies depending on the production method. As long as the above various characteristics are satisfied, the phase structure according to the purpose can be freely given by the production method. There are foaming methods, phase separation methods, dissolution recrystallization methods, stretched pore opening methods, powder sintering methods, etc., among these porous membrane production methods. Among these, phase separation is performed in terms of uniform micropores and cost. The method is preferred.

  The porous film A needs to have a function of closing the pores when the charge / discharge reaction is abnormal (pore closing function). Therefore, the melting point (softening point) of the constituent resin is preferably 70 to 150 ° C, more preferably 80 to 140 ° C, and most preferably 100 to 130 ° C. If the temperature is lower than 70 ° C, the pore blocking function may be exhibited during normal use and the battery may become unusable. Therefore, if the temperature exceeds 150 ° C, the abnormal reaction proceeds sufficiently and the hole blocking function appears. Therefore, safety may not be ensured.

  The film thickness of the porous film A needs to be less than 10 μm. The upper limit of the film thickness is preferably 9.5 μm, more preferably 9 μm. The lower limit of the film thickness is preferably 5 μm, more preferably 6 μm. If the film thickness is less than 5 μm, it may not be possible to retain practical film strength and pore blocking function. If the film thickness is 10 μm or more, the area per unit volume of the battery case is greatly restricted, and will continue in the future. It is not suitable for increasing the capacity of batteries.

  The upper limit of the air permeability resistance (JIS-P8117) of the porous membrane A is preferably 500 seconds / 100 cc Air, more preferably 400 seconds / 100 cc Air, and most preferably 300 seconds / 100 cc Air. The lower limit of the air resistance is preferably 50 seconds / 100 cc Air, more preferably 70 seconds / 100 cc Air, and most preferably 100 seconds / 100 cc Air.

  The upper limit of the porosity of the porous membrane A is 70%, preferably 60%, more preferably 55%. The lower limit of the porosity is 30%, preferably 35%, more preferably 40%. Whether the air resistance is higher than 500 seconds / 100 cc Air or the porosity is lower than 30%, sufficient charge / discharge characteristics of the battery, particularly ion permeability (charge / discharge operating voltage), battery life (electrolysis) (It is closely related to the amount of liquid retained), and if these ranges are exceeded, the battery function may not be fully exhibited. On the other hand, even if the air permeability resistance is lower than 50 seconds / 100 cc Air or the porosity is higher than 70%, sufficient mechanical strength and insulation cannot be obtained, and a short circuit may occur during charging and discharging. Increases nature.

Since the average pore diameter of the porous membrane A greatly affects the pore closing rate, it is 0.01 to 0.3 μm, preferably 0.05 to 0.3 μm, and more preferably 0.1 to 0.2 μm. When the average pore diameter is smaller than 0.01 μm, the anchor effect of the polyamide resin is difficult to obtain, so that sufficient adhesion of the polyamide resin may not be obtained. Is more likely to do. When the average pore diameter is larger than 1.0 μm, there is a possibility that a phenomenon such as a slow response to the temperature of the pore clogging phenomenon or a shift of the pore clogging temperature due to the heating rate to a higher temperature side may occur. Furthermore, it can suppress that a polyamide resin permeate | permeates too much by making an average hole diameter 0.3 micrometer or less.
As for the surface state of the porous membrane A, if the surface roughness (arithmetic average roughness) is in the range of 0.01 to 0.5 μm, the adhesion with the porous membrane B tends to be stronger. When the surface roughness is lower than 0.01 μm, the effect of improving the adhesion is not observed. When the surface roughness is higher than 0.5 μm, the mechanical strength of the porous film A is reduced or the unevenness is transferred to the surface of the porous film B. Sometimes.

Next, the porous membrane B used in the present invention will be described.
The porous membrane B includes a polyamide resin containing an isophorone structure in the amine component, and plays a role of supporting and reinforcing the porous membrane A due to its heat resistance. Therefore, the glass transition temperature of the resin constituting the porous membrane B is preferably 70 ° C. or higher, more preferably 80 ° C. or higher, most preferably 100 ° C. or higher, and the upper limit is not particularly limited. When the glass transition temperature is higher than the decomposition temperature, the decomposition temperature may be in the above range. When the glass transition temperature is lower than 70 ° C., a sufficient heat-resistant film breaking temperature cannot be obtained, and high safety may not be ensured.

Hereinafter, the polyamide resin used for the porous membrane B will be described.
The polyamide resin has, as an amine component, an aliphatic diamine such as ethylenediamine and 1,4-butanediamine; an alicyclic diamine such as cyclohexanediamine, methylcyclohexanediamine, isophoronediamine, norbornanedimethyldiamine, and tricyclodecanedimethyldiamine; p- Aromatic diamines such as phenylenediamine, m-phenylenediamine, xylylenediamine, xylenediamine, 4,4'-diaminodiphenylmethane, 4,4'-diaminodiphenylsulfone, 4,4'-diaminodiphenyl ether can be used. In the present invention, it is necessary to contain an amine component having an isophorone structure. The introduction of such an isophorone structure is particularly effective for suppressing swelling and deterioration with time when the separator is immersed in a non-aqueous electrolyte.

  Here, the proportion of the isophorone structure is preferably in the range of 10 to 100 mol% of the amine component of the polyamide resin, and more preferably in the range of 30 to 100 mol%. When the proportion of the isophorone structure is less than 10 mol%, the above-mentioned electrolytic solution resistance may be lowered.

  In general, the polyamide resin is synthesized by a solution polymerization method such as an acid chloride method using a polyvalent carboxylic acid chloride and a diamine, a diisocyanate method using a polyvalent carboxylic acid and a diisocyanate, or a melt polymerization method. In the case of the present invention, the polyamide resin used for the production of the porous membrane is preferably used in a solution state, and solution polymerization using diamine or diisocyanate is preferable from the viewpoint of production cost.

  The polyvalent carboxylic acid component used for the synthesis of the polyamide resin includes oxalic acid, adipic acid, malonic acid, sebacic acid, azelaic acid, dodecanedicarboxylic acid, dicarboxypolybutadiene, dicarboxypoly (acrylonitrile-butadiene), dicarboxypoly Aliphatic dicarboxylic acids such as (styrene-butadiene), 1,4-cyclohexanedicarboxylic acid, 1,3-cyclohexanedicarboxylic acid, 4,4'-dicyclohexylmethanedicarboxylic acid, alicyclic dicarboxylic acids such as dimer acid, terephthalic acid And aromatic dicarboxylic acids such as isophthalic acid, diphenylsulfone dicarboxylic acid, diphenyl ether dicarboxylic acid and naphthalenedicarboxylic acid. Some of them can be replaced with tricarboxylic acids such as trimellitic acid and trimesic acid, and tetracarboxylic acids such as pyromellitic acid, benzophenone tetracarboxylic acid, biphenyltetracarboxylic acid, and diphenyltetracarboxylic acid. Among these, 1,3-cyclohexanedicarboxylic acid and 1,4-cyclohexanedicarboxylic acid are preferable from the viewpoint of polymerizability, solvent solubility, and resistance to electrolytic solution, and dimer acid and molecular weight of 1000 are preferable from the shutdown characteristics. The above dicarboxypolybutadiene, dicarboxypoly (acrylonitrile butadiene), and dicarboxypoly (styrene-butadiene) are preferred.

  In addition, a urethane group can be introduced into the molecule by replacing a part of the dicarboxylic acid compound with glycol. Examples of glycols include alkylene glycols such as ethylene glycol, propylene glycol, tetramethylene glycol, neopentyl glycol, and hexanediol, polyalkylene glycols such as polyethylene glycol, polypropylene glycol, and polytetramethylene glycol, and one or two of the above dicarboxylic acids. Examples thereof include polyesters having terminal hydroxyl groups synthesized from the above and one or more of the above-mentioned glycols. Among these, polyethylene glycol and polyesters having terminal hydroxyl groups are preferred because of shutdown effect. Moreover, these number average molecular weights are preferably 500 or more, and more preferably 1000 or more. The upper limit is not particularly limited, but is preferably less than 8000.

  When cyclohexanedicarboxylic acid is used as a part of the polyvalent carboxylic acid component, it is preferable to replace 20 to 70 mol% of the polyvalent carboxylic acid component in order to satisfy the solvent solubility and shutdown characteristics. In addition, when a part of the acid component is replaced with at least one member selected from the group consisting of dimer acid, polyalkylene ether, polyester, and butadiene-based rubber containing a carboxyl group, a hydroxyl group, or an amino group at the terminal, It is preferable to replace 1 to 60 mol% of the components.

  As the diamine (diisocyanate) component used for the synthesis of the polyamide resin, the isophorone diamine (diisocyanate) is an essential component, but as a component to replace a part thereof, an aliphatic diamine such as ethylenediamine, propylenediamine, hexamethylenediamine, etc. And alicyclic diamines such as these diisocyanates, 1,4-cyclohexanediamine, 1,3-cyclohexanediamine, and dicyclohexylmethanediamine, and these diisocyanates, m-phenylenediamine, p-phenylenediamine, 4,4'-diaminodiphenylmethane 4,4'-diaminodiphenyl ether, 4,4'-diaminodiphenylsulfone, benzidine, xylylenediamine, naphthalenediamine and other aromatic diamines and their diiso Aneto and the like, reactivity among these, cost, and most preferably dicyclohexylmethane diamine and its diisocyanates terms of electrolyte solution resistance, 4,4'-diaminodiphenylmethane, naphthalene diamines and these diisocyanates are preferred.

  When the polyamide resin is synthesized by solution polymerization, the raw material components are 60 to 200 ° C. in a polar solvent such as N, N′-dimethylformamide, N, N′-dimethylacetamide, N-methyl-2-pyrrolidone, and γ-butyrolactone. It can be easily produced by stirring while heating. In this case, amines such as triethylamine and diethylenetriamine, alkali metal salts such as sodium fluoride, potassium fluoride, cesium fluoride, sodium methoxide, and the like can be used as a catalyst as necessary.

  The polyamide resin preferably has a glass transition temperature of 70 ° C. or higher and a logarithmic viscosity of 0.5 dl / g or higher. If the glass transition temperature is less than 70 ° C., there is a shutdown effect, but the meltdown temperature becomes low, and when used for a separator, the positive electrode and the negative electrode may be short-circuited. On the other hand, the upper limit of the glass transition temperature is preferably less than 400 ° C. in consideration of workability and solvent solubility. On the other hand, when the logarithmic viscosity is less than 0.5 dl / g, there is a risk that the same danger may increase due to a decrease in the melting temperature. Moreover, since the molecular weight is low, the porous membrane may be brittle. On the other hand, the upper limit of the logarithmic viscosity is 2.0 dl / g, more preferably 1.5 dl / g in consideration of processability and solvent solubility.

  The porous membrane B is a polyamide resin solution (varnish) that is soluble in a polyamide resin and dissolved in a solvent miscible with water, applied to a predetermined base film, and mixed with the polyamide resin and water under humidified conditions. It is obtained by phase-separating the solvent to be added, and adding it to a water bath (coagulation bath) to coagulate the polyamide resin. If necessary, a phase separation aid may be added to the varnish.

  Solvents that can be used to dissolve the polyamide resin include N, N-dimethylacetamide (DMAc), N-methyl-2-pyrrolidone (NMP), phosphoric acid hexamethyltriamide (HMPA), N, N-dimethylformamide. (DMF), dimethyl sulfoxide (DMSO), γ-butyrolactone, chloroform, tetrachloroethane, dichloroethane, 3-chloronaphthalene, parachlorophenol, tetralin, acetone, acetonitrile, etc. are listed, and can be freely selected according to the solubility of the resin it can.

  The solid content concentration of the varnish is not particularly limited as long as it can be uniformly applied, but is preferably 2% by weight or more and 50% by weight or less, more preferably 4% by weight or more and 40% by weight or less. When the solid content concentration is less than 2% by weight, the obtained porous membrane B may become brittle. On the other hand, if it exceeds 50% by weight, it may be difficult to control the thickness of the porous membrane B.

  The phase separation aid used in the present invention is water, alkylene glycol such as ethylene glycol, propylene glycol, tetramethylene glycol, neopentyl glycol and hexanediol, polyalkylene glycol such as polyethylene glycol, polypropylene glycol and polytetramethylene glycol, water-soluble Selected from water-soluble polyester, water-soluble polyurethane, polyvinyl alcohol, carboxymethyl cellulose and the like. The amount added is preferably 10 to 90% by weight, more preferably 20 to 80% by weight, and most preferably 30 to 70% by weight, based on the weight of the varnish solution.

  By mixing these phase separation aids in the varnish, it is possible to mainly control the air permeability resistance, the surface porosity, and the layer structure formation rate. When the addition amount is less than the above range, the phase separation rate may not be significantly increased. When the addition amount is more than the above range, the coating liquid becomes cloudy at the mixing stage and the resin component is precipitated. There is a fear.

  Moreover, in order to reduce the heat shrinkage rate of the porous layer B and to impart slipperiness, inorganic particles or heat-resistant polymer particles may be added to the varnish. When adding particles, the upper limit of the amount added is preferably 95% by mass. When the addition amount exceeds 95% by mass, the ratio of the polyamide resin to the total volume of the porous membrane B becomes small, and sufficient adhesion of the polyamide resin to the porous membrane A may not be obtained.

  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 the like. Examples of the heat resistant polymer particles include crosslinked polystyrene particles, crosslinked acrylic resin particles, crosslinked methyl methacrylate particles, benzoguanamine / formaldehyde condensate particles, melamine / formaldehyde condensate particles, and polytetrafluoroethylene particles. .

  The film thickness of the porous membrane B is preferably 1 to 5 μm, more preferably 1 to 4 μm, and most preferably 1 to 3 μm. When the film thickness is thinner than 1 μm, there is a possibility that the film breaking strength and the insulating property when the porous film A is melted / shrinked at a melting point or higher cannot be secured. When the film thickness is thicker than 5 μm, the proportion of the porous membrane A in the composite porous membrane is small, a sufficient pore blocking function cannot be obtained, and abnormal reactions may not be suppressed. Moreover, there is a possibility that the volume of winding becomes large and it is not suitable for increasing the capacity of a battery that will be advanced in the future.

  The porosity of the porous membrane B is preferably 30 to 90%, more preferably 40 to 70%. If the porosity is less than 30%, the electrical resistance of the film increases and it becomes difficult to pass a large current. On the other hand, if it exceeds 90%, the film strength tends to be weak. Moreover, it is preferable that the value measured by the method based on JIS-P8117 is the air permeability resistance of the porous membrane B is 1-2000 second / 100ccAir. More preferably, it is 50-1500 second / 100ccAir, More preferably, it is 100-1000 second / 100ccAir. When the air resistance is less than 1 second / 100 cc Air, the film strength is weak, and when it exceeds 2000 seconds / 100 cc Air, the cycle characteristics may be deteriorated.

  The upper limit of the total thickness of the composite porous membrane obtained by laminating the porous membrane A and the porous membrane B is 13 μm, and more preferably 12 μm. The lower limit of the total thickness is preferably 6 μm or more, more preferably 7 μm or more. If it is thicker than 13 μm, the increase in air resistance may increase, and it may be difficult to avoid a decrease in capacity due to a decrease in the electrode area that can be filled in the container. If the thickness is less than 6 μm, it may be difficult to ensure sufficient mechanical strength and insulation.

  In the composite porous membrane of the present invention, the difference (Y−X) between the air permeability resistance (X seconds / 100 cc Air) of the porous membrane A and the air permeability resistance (Y seconds / 100 cc Air) of the entire composite porous membrane is 20 Second / 100 cc Air ≦ Y−X ≦ 100 seconds / 100 cc Air If Y-X is less than 20 seconds / 100 cc Air, sufficient adhesion of the polyamide resin layer cannot be obtained. On the other hand, if it exceeds 100 seconds / 100 cc Air, the air permeability resistance is significantly increased. As a result, the ion permeability is lowered when the battery is incorporated in the battery, so that the separator is not suitable for a high-performance battery.

  Further, the air resistance of the composite porous membrane is preferably 50 to 600 seconds / 100 cc Air, more preferably 100 to 500 seconds / 100 cc Air, and most preferably 100 to 400 seconds / 100 cc Air. When the value of the air permeability resistance is lower than 50 seconds / 100 cc Air, sufficient insulation cannot be obtained, and foreign matter clogging, short circuit, and film breakage may occur. On the other hand, when the value is higher than 600 seconds / 100 cc Air, the film resistance is high, and charge / discharge characteristics and life characteristics in a practically usable range may not be obtained.

  The upper limit of the porosity of the composite porous membrane used in the present invention is 80%, preferably 70%, more preferably 60%. The lower limit of the porosity is 30%, preferably 35%, more preferably 40%. If the porosity is higher than 80%, sufficient mechanical strength and insulation cannot be obtained, and the possibility of short circuit during charge / discharge increases. On the other hand, if it is lower than 30%, sufficient charge / discharge characteristics of the battery, particularly ion permeability (charge / discharge operating voltage), battery life (intimately related to the amount of electrolyte retained) are not sufficient. If the above range is exceeded, the battery function may not be fully exhibited. The porosity of the composite porous membrane is obtained by calculating the apparent resin density of the composite porous membrane from the resin density and film thickness of the porous membrane A and the porous membrane B, and calculating from the porosity calculation formula described later. Can do.

Next, the manufacturing method of the composite porous membrane of this invention is demonstrated.
In the method for producing a composite porous membrane of the present invention, first, a varnish (polyamide resin solution) is applied on a base film such as a polyester film or a polyolefin film, and then passed through a low humidity zone. During this time, the polyamide resin in the varnish and the solvent in which the resin is dissolved are phase-separated.

  Examples of the method for applying the varnish include reverse roll coating, gravure coating, kiss coating, roll brushing, spray coating, air knife coating, wire barber coating, pipe doctor method, blade coating method, and die coating method. These methods can be carried out alone or in combination.

The low humidity zone in the present invention is a zone whose absolute humidity is adjusted to less than 6 g / m ³ . The upper limit of absolute humidity is preferably 4 g / m ³ , more preferably 3 g / m ³ , and the lower limit is preferably 0.5 g / m ³ , more preferably 0.8 g / m ³ . If the absolute humidity is less than 0.5 g / m ³ , phase separation is not sufficiently performed, so that it is difficult to finally become a porous membrane, and the increase in air resistance may be increased. In addition, when the absolute humidity is 6 g / m ³ or more, the polyamide resin starts to solidify in parallel with the phase separation, and when the porous membrane A is bonded, the polyamide resin does not sufficiently penetrate into the porous membrane A. The adhesion of the polyamide resin cannot be obtained. The passage time in the low humidity zone is preferably 3 seconds or more and 20 seconds or less. If it is less than 3 seconds, the phase separation may not be sufficiently performed. On the other hand, if it exceeds 20 seconds, the solidification of the polyamide resin may proceed excessively.

Next, the coated film is passed through a high humidity zone to form a semi-gel polyamide resin film on the base film. In the present invention, the high humidity zone means that the lower limit of absolute humidity is 6 g / m ³ , preferably 7 g / m ³ , more preferably 8 g / m ³ , and the upper limit of absolute humidity is 25 g / m ³ , preferably 17 g / m ³ . m ³ , more preferably a zone adjusted to 15 g / m ³ . When the absolute humidity is less than 6 g / m ³ , gelation (non-fluidization) is not sufficiently performed. Therefore, when the porous membrane A is bonded, too much penetration of the polyamide resin into the porous membrane A proceeds, Increases the resistance level. If the absolute humidity exceeds 25 g / m ³ , the solidification of the polyamide resin proceeds excessively, the penetration of the polyamide resin into the porous membrane A becomes too small, and sufficient adhesion may not be obtained. The passage time in the high humidity zone is preferably 3 seconds or more and 10 seconds or less. In less than 3 seconds, gelation (non-fluidization) is not sufficiently performed. Therefore, when the porous membrane A is bonded, the penetration of the polyamide resin into the porous membrane A proceeds too much, and the air resistance increases. May increase. On the other hand, if it exceeds 10 seconds, the solidification of the polyamide resin proceeds too much, the penetration of the polyamide resin into the porous membrane A becomes too small, and sufficient adhesion may not be obtained.

  The temperature condition for both the low humidity zone and the high humidity zone is not particularly limited as long as the absolute humidity is within the above range, but is preferably 20 ° C. or more and 50 ° C. or less from the viewpoint of energy saving. The thickness of the substrate film is not particularly limited as long as it can maintain the planarity, but a thickness of 25 μm to 100 μm is preferable. If it is less than 25 μm, sufficient planarity may not be obtained. Moreover, even if it exceeds 100 micrometers, planarity does not improve.

  Next, the porous film A is bonded to the semi-gelled polyamide resin film thus formed so as not to include bubbles. As a method of laminating, a method of laminating a film coming from two directions on the surface of one metal roll is preferable because it causes less damage to the film. Here, the semi-gel form refers to a state in which a region gelled in the process of gelation of the polyamide resin solution due to absorption of moisture in the atmosphere and a region holding the solution state are mixed.

  The porous film A is preferably pasted on the semi-gelled polyamide resin film within at least 10 seconds immediately after passing through the high humidity zone. If it exceeds 10 seconds, solidification of the polyamide resin film proceeds and sufficient adhesion of the porous film B may not be obtained.

  After the formation of the polyamide resin film, the base film may be peeled off. However, in the method of the present invention, it is preferable to bond the porous film A to the polyamide resin film without peeling off the base film. When this method is used, a composite porous membrane can be produced even when a soft porous membrane A that has a low elastic modulus and is necked by the tension during processing is used. Specifically, it can be expected that the composite porous membrane does not wrinkle or bend when passing through the guide roll, and curling during drying can be reduced. At this time, the base material and the composite porous membrane may be wound up at the same time, or after passing through the drying step, the base material and the composite porous membrane may be wound up on separate winding rolls. Is preferable because there is little risk of winding deviation.

  Next, the bonded porous film A and polyamide resin film are immersed in a coagulation bath, and the polyamide resin film is converted into a porous film B by phase conversion. The composition of the coagulation bath is not particularly limited. For example, the coagulation bath may be an aqueous solution containing 1 to 20% by weight, more preferably 5 to 15% by weight of a good solvent for the polyamide resin constituting the porous membrane B. By immersion in the coagulation bath, the porous membrane B is transferred to the porous membrane A over the entire surface, and an unwashed composite porous membrane is obtained. This is because a part of the porous membrane B appropriately bites into the pores of the porous membrane A and the anchor effect is expressed.

  Furthermore, the above-mentioned unwashed porous membrane can be subjected to a washing step using pure water or the like and a drying step using hot air at 100 ° C. or lower, and the final composite porous membrane can be obtained.

  For cleaning, general techniques such as heating, ultrasonic irradiation, and bubbling can be used. Furthermore, in order to keep the concentration in each bath constant and increase the cleaning efficiency, it is effective to remove the solution inside the porous membrane between the baths. Specifically, a method of extruding the solution inside the porous layer with air or an inert gas, a method of physically squeezing out the solution inside the membrane with a guide roll, and the like can be mentioned.

  According to the method of the present invention, even when the thickness of the porous membrane A is less than 10 μm, a composite porous membrane having an excellent balance between adhesion and air resistance can be obtained.

  The composite porous membrane of the present invention can be prepared by using a polyolefin-based porous membrane slit to a target width as the porous membrane A, but it can also be processed subsequently on-line when the polyolefin porous membrane is produced. It is. Here, online refers to the purpose of laminating the porous membrane B continuously after the polyolefin porous membrane manufacturing process (specifically, the drying step after washing), and through the solidification, washing and slitting steps. Means for obtaining a composite porous membrane. By performing the above-mentioned online coating, mass production becomes possible, which is very advantageous in terms of cost.

  Although it is desirable to store the composite porous membrane of the present invention in a dry state, if it is difficult to store in a completely dry state, it is preferable to perform a vacuum drying treatment at 100 ° C. or lower immediately before use.

  The composite porous membrane of the present invention is used for batteries such as nickel-hydrogen batteries, nickel-cadmium batteries, nickel-zinc batteries, silver-zinc batteries, lithium primary batteries and lithium ion secondary batteries, lithium polymer secondary batteries, etc. Although it can be used as a separator, it is particularly preferably used as a separator for a lithium ion secondary battery. Hereinafter, a lithium ion secondary battery will be described as an example.

  In a lithium ion secondary battery, 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 may be a known structure. For example, an electrode structure (coin type) in which disc-shaped positive electrodes and negative electrodes are opposed to each other, an electrode structure in which flat plate-like positive electrodes and negative electrodes are alternately stacked (stacked type), and belt-shaped positive electrodes and negative electrodes are stacked. It can be set as a structure such as a wound electrode structure (winding type).

The positive electrode has a current collector and a positive electrode active material layer containing a positive electrode active material capable of occluding and releasing lithium ions formed on the current collector. Examples of 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, and Fe. , Co, Ni and the like. Preferred examples of the lithium composite oxide among the positive electrode active materials include lithium nickelate, lithium cobaltate, lithium manganate, and a layered lithium composite oxide based on an α-NaFeO ₂ type structure.

The negative electrode has a current collector and a negative electrode active material layer including a negative electrode active material formed on the surface of the current collector. Examples of the negative electrode active material include carbonaceous materials such as natural graphite, artificial graphite, cokes, and carbon black. The electrolytic solution can be obtained by dissolving a lithium salt in an organic solvent. Lithium salts include LiClO ₄ , LiPF ₆ , LiAsF ₆ , LiSbF ₆ , LiBF ₄ , LiCF ₃ SO ₃ , LiN (CF ₃ SO ₂ ) ₂ , LiC (CF ₃ SO ₂ ) ₃ , Li ₂ B ₁₀ Cl ₁₀ , Examples include LiN (C ₂ F ₅ SO ₂ ) ₂ , LiPF ₄ (CF ₃ ) ₂ , LiPF ₃ (C ₂ F ₅ ) ₃ , lower aliphatic carboxylic acid lithium salt, LiAlCl _{4 and the} like. These may be used alone or in admixture of two or more. Examples of the organic solvent include organic solvents having a high boiling point and a high dielectric constant such as ethylene carbonate, propylene carbonate, ethyl methyl carbonate, and γ-butyrolactone, tetrahydrofuran, 2-methyltetrahydrofuran, dimethoxyethane, dioxolane, dimethyl carbonate, diethyl carbonate, and the like. Examples include organic solvents having a low boiling point and a low viscosity. These may be used alone or in admixture of two or more. In particular, a high dielectric constant organic solvent has a high viscosity, and a low viscosity organic solvent has a low dielectric constant. Therefore, it is preferable to use a mixture of both.

  When assembling the battery, the separator (composite porous membrane) is impregnated with the electrolytic solution. Thereby, ion permeability can be imparted to the separator. Usually, the impregnation treatment is performed by immersing the porous membrane in an electrolytic solution at room temperature. For example, when assembling a cylindrical battery, first, a positive electrode sheet, a separator (composite porous membrane), and a negative electrode sheet are laminated in this order, and this laminate is wound from one end to form a wound electrode element. Next, a battery can be obtained by inserting this electrode element into a battery can, impregnating with the above electrolyte, and caulking a battery lid also serving as a positive electrode terminal provided with a safety valve via a gasket.

  Hereinafter, although an example is shown and explained concretely, the present invention is not restrict | limited at all by these examples. In addition, the measured value in an Example was measured with the following method.

(1) Film thickness It measured using the contact-type film thickness meter (Sony Manufacturing Co., Ltd. digital micrometer M-30).

(2) Peel strength at the interface between porous membrane A and porous membrane B Adhesive tape (Nichiban Co., Ltd., No. 405; 24 mm width) was applied to the porous membrane B surface of the separator obtained in the examples and comparative examples. A sample for testing was prepared by cutting into a width of 24 mm and a length of 150 mm.

  Porous film A using a tensile tester [“Tensilon RTM-100” manufactured by A & D Co., Ltd.] under the conditions of 23 ° C. and 50% RH by a peel method (peeling speed 500 mm / min, T-type peeling). And the peel strength at the interface of the porous membrane B were measured. The measurement was performed over time during 100 mm from the start of measurement to the end of measurement, the average value of the measured values was calculated, and converted to a value per 25 mm width to obtain the peel strength. In addition, although the porous film B surface may remain on the porous film A side at the peeling interface, the peeling strength at the interface between the porous film A and the porous film B is also calculated in this case.

(3) Average pore diameter The average pore diameter of the porous membrane A was measured by the following method. The test piece was fixed to the measuring cell using double-sided tape, platinum or gold was vacuum-deposited for several minutes, and the measurement was performed at an appropriate magnification. Arbitrary 10 places observed most foremost on the image obtained by SEM measurement were selected, and the average value of the pore diameters at these 10 places was defined as the average pore diameter of the test piece. In addition, when the hole was not substantially circular, the value obtained by adding the major axis and the minor axis and dividing by 2 was defined as the hole diameter.

(4) Air permeability resistance Using a Gurley-type densometer type B manufactured by Tester Sangyo Co., Ltd., the composite porous membrane is fixed so that no wrinkles are formed between the clamping plate and the adapter plate. Measured according to P-8117. Two samples of 10 cm square were prepared as samples, and for each sample, a total of 10 points were measured with the central part and four corners of the sample as measurement points, and the average value of 10 points was measured for air resistance [seconds / second] 100 cc Air]. When the length of one side of the sample is less than 10 cm, a value obtained by measuring 10 points at intervals of 5 cm may be used.

(5) Logarithmic viscosity A solution obtained by dissolving 0.5 g of polyamide resin in 100 ml of NMP was measured at 25 ° C using an Ubbelohde viscosity tube.

(6) Glass transition temperature A polyamide resin solution or a resin solution obtained by immersing a composite porous membrane in a good solvent and dissolving only the polyamide resin membrane is subjected to PET film (Toyobo E5001) or polypropylene film (Toyobo Co., Ltd.) using an applicator. Pyrene-OT) is applied with a suitable gap, pre-dried at 120 ° C. for 10 minutes, peeled off, fixed to a metal frame of an appropriate size with a heat-resistant adhesive tape, and further dried at 200 ° C. for 12 hours under vacuum. As a result, a dry film was obtained. A test piece having a width of 4 mm and a length of 21 mm was cut from the obtained dry film, and the measurement length was 15 mm, using a dynamic viscoelasticity measuring apparatus (DVA-220 manufactured by IT Measurement Control), 110 Hz, temperature increase rate of 4 ° C. / The storage elastic modulus (E ′) was measured in the range from room temperature to 450 ° C. under the condition of minutes. At the refraction point of the storage elastic modulus (E ′) at this time, the temperature at the intersection of the extended line of the base line below the glass transition temperature and the tangent showing the maximum inclination above the refraction point was defined as the glass transition temperature.

(7) Porosity A 10 cm square sample was prepared, its sample volume (cm ³ ) and mass (g) were measured, and the porosity (%) was calculated from the obtained result using the following formula. Note that the sample volume (cm ³ ) of the 10 cm square sample can be obtained by 10 (cm) × 10 (cm) × the thickness (cm) of the porous film A.
Porosity = (1−mass / (resin density × sample volume)) × 100

Example 1
In a four-necked flask equipped with a thermometer, a cooling pipe, and a nitrogen gas introduction pipe, 1 mol of sebacic acid, 1 mol of isophorone diisocyanate (IPDI), and 0.02 mol of potassium fluoride are added so that the solid content concentration becomes 50%. -The mixture was charged with methyl-2-pyrrolidone, stirred at 180 ° C for 5 hours, and then diluted with N-methyl-2-pyrrolidone to a solid content concentration of 10% to synthesize a polyamide resin solution (a). The obtained polyamide resin had a logarithmic viscosity of 0.65 dl / g and a glass transition temperature of 130 ° C.

48 parts by mass of this polyamide resin solution (a) was diluted with 39 parts by mass of N-methyl-2-pyrrolidone, 13 parts by mass of ethylene glycol was further added, and varnish (a) (solid content concentration 5.3% by weight) was added. Prepared. A varnish (a) was applied to the corona-treated surface of a polyethylene terephthalate resin film (base film; E5101 manufactured by Toyobo Co., Ltd.) having a thickness of 50 μm by a blade coating method, and the humidity was low at 25 ° C. and an absolute humidity of 1.8 g / m ³ . The zone was passed for 8 seconds, and subsequently passed through a high humidity zone with a temperature of 25 ° C. and an absolute humidity of 12 g / m ³ for 5 seconds to form a semi-gel polyamide resin film. 1.7 seconds after the heat-resistant resin film exits the high humidity zone, porous film A (polyethylene porous film, thickness 9 μm, porosity 45%, average pore diameter 0.15 μm, air resistance 240 sec / 100 cc Air) ) Is placed on the above semi-gelled polyamide resin film, allowed to enter an aqueous solution containing 5% by weight of N-methyl-2-pyrrolidone, then washed with pure water, and then passed through a hot air drying oven at 70 ° C. And dried to obtain a composite porous membrane having a final thickness of 11.6 μm.

Example 2
A composite porous membrane was obtained in the same manner as in Example 1 except that the absolute humidity of the low humidity zone was 4.0 g / m ³ .

Example 3
A composite porous membrane was obtained in the same manner as in Example 1 except that the absolute humidity of the low humidity zone was 5.5 g / m ³ .

Example 4
A composite porous membrane was obtained in the same manner as in Example 1 except that the absolute humidity of the high humidity zone was 7.0 g / m ³ .

Example 5
A composite porous membrane was obtained in the same manner as in Example 1 except that the absolute humidity in the high humidity zone was 16.0 g / m ³ .

Example 6
Example 1 except that the passage times of the low-humidity zone and the high-humidity zone were 5.3 seconds and 3.0 seconds, respectively, and the time from the exit of the high-humidity zone to the bonding of the porous membrane A was 1.1 seconds. In the same manner, a composite porous membrane was obtained.

Example 7
Example 1 except that the passage time of the low humidity zone and the high humidity zone was 16.0 seconds and 10.0 seconds, respectively, and the time until the porous membrane A was bonded from the exit of the high humidity zone was 3.4 seconds. In the same manner, a composite porous membrane was obtained.

Example 8
A composite porous membrane A was prepared in the same manner as in Example 1 except that a polyethylene porous membrane having a thickness of 9.5 μm, a porosity of 40%, an average pore diameter of 0.15 μm, and a gas permeability of 320 seconds / 100 cc Air was used as the porous membrane A. A membrane was obtained.

Example 9
A composite porous membrane A was prepared in the same manner as in Example 1 except that a polyethylene porous membrane having a thickness of 7.0 μm, a porosity of 40%, an average pore diameter of 0.15 μm, and an air resistance of 220 seconds / 100 cc Air was used as the porous membrane A. A membrane was obtained.

Example 10
The acid component of Example 1 is 0.5 mol of isophthalic acid, 0.5 mol of sebacic acid, 0.505 mol of isophorone diisocyanate, 0.505 mol of diphenylmethane-4,4'-diisocyanate (MDI), 0.02 of potassium fluoride. Mole was charged with N-methyl-2-pyrrolidone so as to have a solid content concentration of 50%, reacted at 120 ° C. for 1 hour and further at 180 ° C. for 3 hours, and then cooled, while cooling with N-methyl-2-pyrrolidone The polyamide resin solution (b) was synthesized by diluting to a solids concentration of 10%. The obtained polyamide resin had a logarithmic viscosity of 0.7 dl / g and a glass transition temperature of 135 ° C. A composite porous membrane was obtained in the same manner as in Example 1 except that the varnish (b) (solid content concentration 5.3 wt%) obtained by replacing the polyamide resin solution (a) with the polyamide resin solution (b) was used.

Example 11
32.6 parts by mass of the polyamide resin solution (a) and 10.5 parts by mass of alumina particles having an average particle size of 0.5 μm were diluted with 48.4 parts by mass of N-methyl-2-pyrrolidone, and further ethylene glycol 8.5. A mass part was added, and it was put into a polypropylene container together with zirconium oxide beads (trade name “Traceram beads”, diameter 0.5 mm, manufactured by Toray Industries, Inc.), and dispersed for 6 hours with a paint shaker (manufactured by Toyo Seiki Seisakusho). Subsequently, it filtered with the filter of 5 micrometers of filtration limits, and prepared varnish (c) (solid content concentration 31.0 weight%). A composite porous membrane was obtained in the same manner as in Example 1 except that the varnish (a) was changed to the varnish (c).

Example 12
Varnish (d) (solid content concentration 31.0) in the same manner as in Example 11 except that the alumina particles were changed to titanium oxide particles (trade name “KR-380”, average particle diameter 0.38 μm, manufactured by Titanium Industry Co., Ltd.). % By weight). A composite porous membrane was obtained in the same manner as in Example 11 except that the varnish (a) was replaced with the varnish (d).

Example 13
A composite porous membrane was obtained in the same manner as in Example 1 except that the amount of varnish (a) applied was adjusted to a final thickness of 10.3 μm.

Example 14
The composite porous membrane A was composite porous in the same manner as in Example 1 except that a polyethylene porous membrane having a thickness of 6.5 μm, a porosity of 38%, an average pore diameter of 0.15 μm, and a gas permeability resistance of 210 seconds / 100 cc Air was used. A membrane was obtained.

Example 15
A composite porous membrane was obtained in the same manner as in Example 1 except that the absolute humidity of the low-humidity zone was 1.2 g / m ³ .

Comparative Example 1
A composite porous membrane was obtained in the same manner as in Example 1 except that the temperature of the low humidity zone was 25 ° C. and the absolute humidity was 7.0 g / m ³ .

Comparative Example 2
A composite porous membrane was obtained in the same manner as in Example 1 except that the high humidity zone was set to a temperature of 25 ° C. and an absolute humidity of 5.0 g / m ³ .

Comparative Example 3
A varnish (a) was applied to the porous membrane A (made of polyethylene, thickness 9 μm, porosity 45%, average pore diameter 0.15 μm, air permeability 240 sec / 100 cc Air) by a blade coating method, and the temperature was 25 ° C. A low humidity zone with an absolute humidity of 1.8 g / m ³ was passed in 8 seconds, and then a high humidity zone with a temperature of 25 ° C. and an absolute humidity of 12 g / m ³ was passed in 5 seconds. Next, after 2 seconds, it was allowed to enter an aqueous solution containing 5% by weight of N-methyl-2-pyrrolidone, then washed with pure water, and then dried by passing through a hot air drying oven at 70 ° C. to obtain a final thickness of 11 A composite porous membrane of 8 μm was obtained.

Comparative Example 4
Porous membrane A (made of polyethylene, thickness 9 μm, porosity 45%, average pore diameter 0.15 μm, air resistance 240 sec / 100 cc Air) was previously immersed in N-methyl-2-pyrrolidone to saturate the pores. A composite porous membrane was obtained in the same manner as in Comparative Example 3 except that it was used by being filled with N-methyl-2-pyrrolidone.

Comparative Example 5
Varnish (a) was applied to the corona-treated surface of a polyethylene terephthalate resin film (Toyobo E5101, thickness 50 μm) by the blade coating method, followed by a high humidity zone with a temperature of 25 ° C. and an absolute humidity of 18.4 g / m ^3. Passed in 30.0 seconds, and after 1.7 seconds, porous film A was laminated with a porous film made of polyethylene having a thickness of 10 μm, porosity of 47%, average pore diameter of 0.20 μm, and air resistance of 80 seconds / 100 cc Air Obtained a composite porous membrane in the same manner as in Example 1.

Comparative Example 6
A composite porous membrane was obtained in the same manner as in Example 1 except that the absolute humidity in the high-humidity zone was 25.5 g / m ³ .

Comparative Example 7
A composite porous membrane was obtained in the same manner as in Example 1 except that the coating amount of varnish (a) was adjusted to a final thickness of 14.4 μm.

Comparative Example 8
A polyamide resin solution (c) was synthesized under the same conditions as in Example 1 except that 1.02 mol of sebacic acid and 1 mol of IPDI were used. The obtained polyamide resin had a logarithmic viscosity of 0.31 dl / g and a glass transition temperature of 128 ° C. A composite porous membrane was obtained in the same manner as in Example 1 except that varnish (e) (solid content concentration 5.3 wt%) in which the polyamide resin solution (a) was replaced with the polyamide resin solution (c) was used.

  Table 1 shows the production conditions of the composite porous membranes of Examples 1 to 15 and Comparative Examples 1 to 8, and the characteristics of the porous membrane A and the composite porous membrane.

The composite porous membrane of the present invention has both excellent adhesion to the polyamide resin layer and small increase in air resistance even when the film thickness is further reduced in the future. It is suitable for ion permeability and high-speed workability in the battery assembly process, and particularly suitable for a separator for a lithium ion secondary battery.

Claims (7)

A composite porous membrane used as a battery separator, wherein a porous membrane A comprising a polyolefin resin and a porous membrane B containing a polyamide resin containing an isophorone structure as an amine component are laminated, The composite porous membrane, wherein the porous membrane satisfies the following formulas (A) to (F):
Thickness of porous membrane A <10 μm Formula (A)
0.01 μm ≦ average pore diameter of porous membrane A ≦ 0.3 μm
... Formula (B)
30% ≦ Porosity of porous membrane A ≦ 70% Formula (C)
Total thickness of composite porous membrane ≦ 13 μm Formula (D)
Peel strength at the interface between porous membrane A and porous membrane B ≧ 1.0 N / 25 mm
... Formula (E)
20 ≦ Y−X ≦ 100 Formula (F)
(X is the air permeability resistance of the porous membrane A (second / 100 cc Air), Y is the air resistance of the entire composite porous membrane (second / 100 cc Air))   The composite porous membrane according to claim 1, wherein the polyamide resin contains an isophorone structure in a proportion of 10 to 100 mol% with respect to the amine component.   The composite porous membrane according to claim 1 or 2, wherein the air permeability resistance of the composite porous membrane is 50 to 600 seconds / 100 cc Air. The method for producing a composite porous membrane according to any one of claims 1 to 3, comprising the following steps (i) and (ii).
Step (i): After applying the polyamide resin solution on the base film, it is passed through a low humidity zone having an absolute humidity of less than 6 g / m ³ , and then high humidity having an absolute humidity of 6 g / m ³ or more and 25 g / m ³ or less. A step of forming a polyamide resin film on the base film through the zone, and a step (ii): the polyamide resin film formed in the step (i) and the porous film A made of a polyolefin-based resin are bonded together Then, a step of immersing in a coagulation bath to convert the polyamide resin film into a porous film B, washing and drying to obtain a composite porous film.   The method for producing a composite porous membrane according to claim 4, wherein the base film is peeled after obtaining the composite porous membrane in the step (ii).   6. The method for producing a composite porous membrane according to claim 4, wherein the base film is a polyester film or a polyolefin film having a thickness of 25 to 100 [mu] m.   The passing time in the low humidity zone is 3 seconds or more and 20 seconds or less in the step (i), and the passing time in the high humidity zone is 3 seconds or more and 10 seconds or less. The manufacturing method of the composite porous membrane as described.