JP5040058B2 - Porous membrane, method for producing the same, and lithium ion secondary battery using the same - Google Patents

Description

  The present invention relates to a polyamide-imide porous membrane that exhibits excellent shutdown temperature characteristics and high meltdown temperature characteristics as a separator for lithium ion secondary batteries that are required to improve safety, a method for producing the same, and lithium using the same The present invention relates to an ion secondary battery.

  In recent years, with the development of electronic portable devices, batteries with high energy density and high electromotive force have been developed. Among them, nonaqueous electrolyte batteries, particularly lithium ion secondary batteries, have been vigorously developed from the viewpoint of high electromotive force. One of the problems with such non-aqueous electrolyte batteries is the danger of using flammable organic solvents. When both electrodes of the battery are short-circuited and a decomposition reaction of the battery contents occurs, the contents are ejected due to a rapid temperature rise inside the battery. In order to solve such problems, there are currently attachment of a safety valve and provision of a shutdown function by a separator containing a meltable component.

  However, the safety valve is not an essential protective measure against a short circuit, but only relieves a sudden pressure increase inside the battery.

  On the other hand, the shutdown function of the separator uses a porous film made of a heat-meltable material. When the temperature inside the battery reaches a certain temperature due to a short circuit or the like, By blocking, the ionic conductivity is hindered and the battery reaction that causes heat generation is suppressed. As such a separator, a porous membrane of an olefin polymer material disclosed in Patent Documents 1 to 3 is disclosed. However, when such a heat-meltable material is used, even if the shutdown function works due to heat rise, if there is a further temperature rise, the film itself melts and the isolation between the electrodes, which is the original function, is impaired. End up. This is a phenomenon called meltdown, which is not preferable for a battery. It has been proposed to widen the range of the shutdown temperature as a remedy for such problems. For example, as disclosed in Patent Documents 4 to 7 and the like, it is a technique of laminating and coating a heat-meltable material on a porous film or a nonwoven fabric substrate. However, these preparation methods may be complicated and an insulation property at the time of shutdown is not necessarily obtained.

Japanese Patent No. 2642206 JP-A-6-212006 Japanese Patent Laid-Open No. 8-138643 Japanese Patent Publication No. 4-1692 JP-A-60-52 JP 61-232560 A Japanese Patent Laid-Open No. 10-6453

  The present invention has been made in view of such circumstances, and an object of the present invention is to provide an inexpensive separator that has excellent shutdown characteristics and melt-down characteristics, which are superior to conventional porous membrane separators, and is excellent in insulation. .

  As a result of intensive studies to achieve the above object, the present invention is excellent in safety and cycle durability by using a porous polyamideimide resin film alone or in combination with other materials as a separator. It was found that a lithium ion secondary battery was obtained. That is, this invention is the following porous membrane, its manufacturing method, and a lithium ion secondary battery using the same.

(1) Glass transition temperature is 70 ° C. or higher, logarithmic viscosity is 0.5 dl / g or higher, and the total film thickness is 5 including the polyamideimide resin layer having the following structural formulas (I) and (II) as essential components. ˜100 μm porous membrane.

(2) A part of the acid component of the polyamide-imide resin is at least one selected from the group consisting of dimer acid, polyalkylene ether, polyester, and butadiene rubber containing any one of carboxyl group, hydroxyl group and amino group at the terminal. The porous membrane according to claim 1, which is a substituted copolymerized polyamideimide resin.

(3) A composite porous membrane according to (1) or (2), wherein a polyamideimide resin layer and a polyolefin-based porous membrane are combined.

(4) The porous film according to any one of claims 1 to 3, which has an air permeability of 1 to 2000 sec / 100 cc Air.

(5) A lithium ion secondary battery comprising the porous film according to any one of claims 1 to 4 interposed as a separator between a positive electrode and a negative electrode capable of inserting and extracting lithium ions.

(6) After applying or immersing the polyamideimide resin solution according to claim 1 or 2 on a substrate, the solution is miscible with the solvent in which the polyamideimide resin is dissolved, but is a poor solvent for the polyamideimide resin. A method for producing a porous membrane that is solidified by being introduced into the inside.

(7) After applying or immersing the polyamideimide resin solution according to claim 1 or 2 on one or both surfaces of the polyolefin-based porous membrane, it is mixed with a solvent in which the polyamideimide resin is dissolved. Is a method for producing a composite porous membrane that is poured into a poor solvent and solidified.

  The present invention provides lithium ion excellent in balance between shutdown characteristics and meltdown characteristics by using a polyamideimide resin porous film having a specific structure or a composite porous film in which a polyamideimide resin porous film and a polyolefin film are laminated. A separator for a secondary battery can be provided.

  The present invention will be described in detail below. The polyamideimide resin used in the present invention contains the following structural formulas (I) and (II) as essential components. The total amount of the formula (I) and the formula (II) is preferably 20 mol% or more, more preferably 40 mol% or more, further preferably 50 mol% or more, most preferably, when the total of all components is 100 mol%. Is 60 mol% or more.

  Here, the molar ratio of the formula (I) and the formula (II) is in the range of 90/10 to 10/90, preferably in the range of 85/15 to 30/70, and more preferably in the range of 80/20 to 50/50. This is because when the ratio of formula (I) is 90 or more, the solvent solubility is lowered and a stable solution may not be obtained, and when it is 10 or less, the strength when formed into a porous film may be insufficient. .

  In general, the polyamideimide resin is synthesized by a conventional method such as an acid chloride method using trimellitic acid chloride and diamine or a diisocyanate method using trimellitic anhydride and diisocyanate, but the diisocyanate method is preferable from the viewpoint of production cost. .

  Although the acid component used for the synthesis | combination of the polyamideimide resin in this invention is trimellitic anhydride (chloride), the one part can be substituted by another polybasic acid or its anhydride. For example, tetracarboxylic acids such as pyromellitic acid, biphenyltetracarboxylic acid, biphenylsulfonetetracarboxylic acid, benzophenonetetracarboxylic acid, biphenylethertetracarboxylic acid, ethylene glycol bistrimellitate, propylene glycol bistrimellitate and their anhydrides, Aliphatic dicarboxylic acids such as oxalic acid, adipic acid, malonic acid, sebacic acid, azelaic acid, dodecanedicarboxylic acid, dicarboxypolybutadiene, dicarboxypoly (acrylonitrile-butadiene), dicarboxypoly (styrene-butadiene), 1,4 -Cyclohexanedicarboxylic acid, 1,3-cyclohexanedicarboxylic acid, 4,4'-dicyclohexylmethanedicarboxylic acid, alicyclic dicarboxylic acids such as dimer acid, terephthalic acid, Le acid, diphenyl sulfone dicarboxylic acid, diphenylether dicarboxylic acid, and aromatic dicarboxylic acids such as naphthalene dicarboxylic acid. Among these, 1,3-cyclohexanedicarboxylic acid and 1,4-cyclohexanedicarboxylic acid are preferable from the viewpoint of the resistance to electrolytic solution, and dimer acid, dicarboxypolybutadiene having a molecular weight of 1000 or more and dicarboxypoly (acrylonitrile) from the shutdown characteristics. Butadiene) and dicarboxypoly (styrene-butadiene) are preferred.

  In addition, a urethane group can be introduced into the molecule by replacing part of the trimellitic 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 more of the above dicarboxylic acids. And polyesters having terminal hydroxyl groups synthesized from one or two or more of the above-mentioned glycols. Among these, polyethylene glycol and polyesters having terminal hydroxyl groups are preferred because of the 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 replacing a part of the acid component with at least one of the group consisting of dimer acid, polyalkylene ether, polyester and butadiene rubber containing any of carboxyl group, hydroxyl group and amino group at the end, 1 to 60 mol% is preferably replaced.

  The diamine (diisocyanate) component used in the synthesis of the polyamideimide resin of the present invention includes o-tolidine and tolylenediamine described in the above formulas (I) and (II) as essential components, part of which. Aliphatic diamines such as ethylenediamine, propylenediamine, and hexamethylenediamine and their diisocyanates, alicyclic diamines such as 1,4-cyclohexanediamine, 1,3-cyclohexanediamine, and dicyclohexylmethanediamine, and their diisocyanates, m-phenylenediamine, p-phenylenediamine, 4,4'-diaminodiphenylmethane, 4,4'-diaminodiphenyl ether, 4,4'-diaminodiphenylsulfone, benzidine, xylylenediamine, naphthalenediamine Aromatic diamines and diisocyanates thereof, and the like. Among them, dicyclohexylmethanediamine and diisocyanates thereof are most preferable from the viewpoint of reactivity, cost, and electrolyte resistance, and 4,4′-diaminodiphenylmethane, naphthalenediamine. And these diisocyanates are also preferred.

  The polyamideimide resin used in the present invention is stirred while heating at 60 to 200 ° C. in a polar solvent such as N, N′-dimethylformamide, N, N′-dimethylacetamide, N-methyl-2-pyrrolidone, and γ-butyrolactone. By doing so, it can be easily manufactured. 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 polyamideimide resin used in the present invention 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 is preferably less than 400 ° C. in consideration of workability and solvent solubility. Further, even when the logarithmic viscosity is less than 0.5 dl / g, the porous film becomes brittle because the similar danger increases due to the decrease in melting temperature and the molecular weight is low. On the other hand, the upper limit is preferably less than 2.0 dl / g in consideration of processability and solvent solubility.

  Next, a method for producing a polyamideimide porous membrane will be described. The production of the porous membrane of the present invention is not particularly limited, but after coating the polyamideimide polymerization solution on a substrate such as a polyester film to a predetermined thickness, or extruding the polymerization solution from a slit die into a film, The polyamidoimide resin is mixed with a dissolving solvent, but it is preferable that the polyamidoimide resin is put into a poor solvent and solidified. In addition, the poor solvent said here shall not be able to melt | dissolve this polyamidoimide resin in 25weight% at a 5 weight% density | concentration.

  As described above, amide solvents such as N-methyl-2-pyrrolidone, dimethylacetamide, and N, N′-dimethylformamide are mainly used as the solvent for dissolving the polyamideimide resin. It is possible to add alcohols such as methanol, ethanol, propyl alcohol, ethylene glycol, diethylene glycol, polyethylene glycol and polypropylene glycol, and ketones such as acetone and methyl ethyl ketone to adjust the pore size and pore size distribution. . These additives are 5 to 300 parts, preferably 10 to 200 parts, more preferably 20 to 100 parts with respect to 100 parts of the polyamideimide resin solution.

  The coagulation bath used when producing the porous material of the present invention is preferably a solution mainly composed of water. This coagulation bath can be mixed with other solvents miscible with water in order to adjust the coagulation rate, the pore size of the porous membrane and its distribution. Such solvents include alcohols such as methanol, ethanol, propyl alcohol, ethylene glycol, propylene glycol, diethylene glycol and polyethylene glycol, ketones such as acetone and methyl ethyl ketone, N, N′-dimethylformamide, N, N′-dimethyl. Examples include amide solvents such as acetamide and N-methyl-2-pyrrolidone. Among these, glycols such as ethylene glycol and polyethylene glycol and N-methyl-2- Amide solvents such as pyrrolidone, N, N′-dimethylacetamide, and N, N′-dimethylformamide are preferred. The amount of these solvents added is 5 to 500 parts, preferably 10 to 400 parts, and more preferably 20 to 300 parts with respect to 100 parts of water. The amount of the additive to the coagulation bath is not particularly limited, but is 5 to 500 parts, preferably 10 to 400 parts, more preferably 20 to 300 parts with respect to 100 parts of water.

  The polyamideimide porous membrane may be a single layer or a laminate, but the total film thickness is 5 to 100 μm, preferably 10 to 70 μm, and more preferably 15 to 50 μm. If the film thickness is 5 μm or less, the film becomes weak and may break. Conversely, when the film thickness exceeds 100 μm, the cycle characteristics may deteriorate. The porosity of the polyamideimide porous membrane is preferably 30 to 90%. More preferably, it is 40 to 70%. When the porosity is 30% or less, the electric resistance of the film becomes high and it becomes difficult to flow a large current. On the other hand, if it is 90% or more, the film strength becomes weak. The air permeability, which is a measure of the pore diameter, is preferably 1 to 2000 sec / 100 cc Air measured by a method based on JIS-P8117. More preferably, it is 50-1500 sec / 100 cc Air, More preferably, it is 100-1000 sec / 100 cc Air. When the air permeability is less than 1 sec / 100 cc Air, the film strength becomes weak, and when it exceeds 2000 sec / 100 cc Air, the cycle characteristics may be deteriorated.

  The polyamideimide porous membrane thus produced exhibits excellent shutdown characteristics and meltdown characteristics even when used alone as a separator. In particular, the effect is remarkable in the case of a porous film made of a polyamideimide resin in which a butadiene rubber having a number average molecular weight of 1000 or more, polyalkylene glycol, polyester, or the like is copolymerized in a block shape. The upper limit of the number average molecular weight is preferably less than 8000 considering the glass transition temperature of the polyamideimide resin.

  Another feature of the present invention is that a polyamide-imide porous membrane can be used in combination with a polyolefin-based porous membrane. The polyolefin-based porous membrane is a polyethylene or polypropylene film produced by, for example, the stretch opening method or the phase separation method described in 7th Polymer Material Forum (1998) Abstract 1 BIL09. When the polyamide-imide porous membrane and the polyolefin porous membrane are laminated, the polyamide-imide porous membrane is A, and the polyolefin-based porous membrane is B. A / B, A / B / A or B / A / B It becomes the composition of.

The production of these composite porous membranes is not particularly limited, but the following method is preferred.
(1) A polyamide-imide porous membrane and a polyolefin porous membrane are simply stacked.
(2) Using a polyolefin porous membrane as a support, impregnating or coating one or both sides with a polyamideimide resin solution, and putting it in a coagulation bath by the same method as described above, to solidify.
(3) Combine (1) and (2) above.

  In the case of these composite porous membranes, the total film thickness is 10 to 100 μm, preferably 15 to 70 μm. The porosity is preferably 30 to 80% and the air permeability is preferably 1 to 2000 sec / 100 cc Air.

  The lithium ion secondary battery using the polyamideimide porous membrane of the present invention configured as described above as a separator exhibits the same battery performance as before, and obtains a safe battery excellent in shutdown characteristics and meltdown characteristics. Can do. The lithium ion secondary battery according to the present invention can be produced according to a conventional method except that the porous membrane of the present invention is used as a separator.

  That is, a material containing lithium can be used as the positive electrode active material, a material that can store and release lithium as ions can be used as the negative electrode, and an organic solvent solution of an electrolyte composed of a compound containing lithium and fluorine can be used as the electrolytic solution.

  Specifically, lithium metal oxides such as lithium cobaltate and lithium manganate that can insert and remove lithium ions can be used as the positive electrode active material. A known active carbon, various cokes, carbon black, a binder, a solvent, and the like are blended into the positive electrode active material as a conductive agent, and this dispersion is applied to a current collector such as aluminum and dried to form a positive electrode material. Can do.

  Coke, graphite, amorphous carbon, etc. are used as the negative electrode active material, and these are applied to a current collector such as a copper foil with a dispersion composed of a binder and an organic solvent, and dried to form a negative electrode material. it can.

Examples of the electrolyte used for the electrolytic solution include LiClO ₄ , LiAsF ₆ , LiPF ₄ , LiBF ₄ , LiBr, LiCF ₃ SO ₃ , and the like. Examples of the organic solvent include propylene carbonate, ethylene carbonate, γ-butyrolactone, dimethyl One or more of carbonate, ethyl methyl carbonate, 1,2-dimethoxyethane, 1,2-diethoxyethane, tetrahydrofuran and the like are used.

EXAMPLES Hereinafter, although an Example demonstrates this invention further in detail, this invention is not restrict | limited by these Examples.
In addition, the measured value in an Example was measured with the following method.

Logarithmic viscosity: A solution obtained by dissolving 0.5 g of polyamideimide resin in 100 ml of N-methyl-2-pyrrolidone was kept at 30 ° C. and measured using an Ubbelohde viscosity tube.

Glass transition temperature: The inflection point of the loss elastic modulus of dynamic viscoelasticity measured by applying a vibration of a frequency of 110 Hz to a polyamideimide film having a measurement width of 4 mm and a length of 15 mm, using a DVE-V4 rheospectr made by Rheology. The glass transition temperature was taken.

Film thickness: The polyamideimide porous film was measured with a SONY μ-meter.

Porosity: The average film thickness (At) and weight (Aw) of about 25 μm film (A) prepared by casting and drying from a polyamideimide resin solution were measured and coagulated in water from the same polyamideimide resin solution. The porosity was calculated from the average film thickness (Bt) of the porous film (B) thus prepared and the weight (Bw) of 10 cm □ by the following formula.
Porosity = [1- (Bw / Bt) / (Aw / At)] × 100 (%)

Shutdown temperature characteristics: A porous membrane filled with 1 mol / l of lithium tetrafluoroborate dissolved in propylene carbonate was used and measured at an AC frequency of 1 kHz, an AC amplitude of 100 mV, and a heating rate of 2 ° C./min. The temperature at which the rise in impedance value due to temperature rise once becomes 100 Ωcm ² is the shutdown start temperature, and the temperature at which the impedance value exceeds 1 kΩcm ² , then rises and decreases again to 1 kΩcm ² is the meltdown temperature. It was.

[Example 1]
In a four-necked flask equipped with a thermometer, a condenser tube, and a nitrogen gas inlet tube, 1 mole of trimellitic anhydride (TMA), 0.8 mole of o-tolidine diisocyanate (TODI), 2,4-tolylene diisocyanate (TDI) ) 0.2 mol and 0.01 mol of potassium fluoride were charged together with N-methyl-2-pyrrolidone so that the solid content concentration was 20%, stirred at 100 ° C. for 5 hours, and then the solid content concentration was 10%. In this way, a polyamide-imide resin was synthesized by diluting with N-methyl-2-pyrrolidone. The obtained polyamideimide resin had a logarithmic viscosity of 1.35 dl / g and a glass transition temperature of 310 ° C.
A dope in which 20 parts of polyethylene glycol # 400 is blended with 100 parts of this polyamideimide resin solution is applied to a commercial separator (polyolefin porous film manufactured by Tonen Chemical Co., Ltd .: 25 μm) so that the film thickness becomes 1 μm. After being immersed for about 3 minutes, it was fixed with a metal frame and dried at 100 ° C. for 10 minutes. The air permeability of the obtained composite porous membrane was 340 sec / 100 cc Air. The shutdown temperature of this film was 121 ° C., and the meltdown temperature was 200 ° C. or higher. Using this porous membrane as a separator, a positive electrode using lithium cobaltate as a positive electrode active material, acetylene black as a conductive agent, polyvinylidene fluoride as a binder, a negative electrode active material mixed with graphite and amorphous carbon, and polyvinylidene fluoride A coin-type battery was prepared using a negative electrode as a binder and Sollite (manufactured by Mitsubishi Chemical) as an electrolytic solution, and the battery characteristics were evaluated. Compared to a commercially available separator (polyolefin porous membrane manufactured by Tonen Chemical Co., Ltd .: 25 μm) alone, the discharge capacity and cycle characteristics were almost the same.

[Example 2]
Solid under the same conditions as in Example 1 except that the acid component of Example 1 was TMA 0.9 mol and dicarboxypoly (acrylonitrile-butadiene) rubber (Ube Industries Hiker CTBN 1300 × 13: molecular weight 3500) was 0.1 mol. A polyamideimide resin having a partial concentration of 10% was synthesized. The obtained polyamidoimide resin had a logarithmic viscosity of 0.65 dl / g and a glass transition temperature of 213 ° C. A composite porous membrane was prepared in the same manner as in Example 1 using a solution in which 20 parts of polyethylene glycol # 400 was blended with 100 parts of this polyamideimide resin solution. The composite porous membrane had a thickness of 27 μm, an air permeability of 460 sec / 100 cc Air, a shutdown temperature of 120 ° C., and a meltdown temperature of 200 ° C. or higher.

[Example 3]
Using the same apparatus as in Example 1, 0.94 mol of TMA, 0.06 mol of polypropylene glycol having a molecular weight of 2000, 0.5 mol of TODI, and 0.5 mol of TDI were added to N, N′-dimethyl so that the solid concentration would be 30%. After charging with acetamide and reacting at 140 ° C. for 3 hours, a polyamideimide resin was synthesized by diluting with N, N′-dimethylacetamide so that the solid content concentration would be 10%. The obtained polyamideimide resin had a logarithmic viscosity of 0.63 dl / g and a glass transition temperature of 198 ° C. A composite porous membrane was prepared in the same manner as in Example 1 using a solution in which 20 parts of polyethylene glycol # 400 was blended with 100 parts of this polyamideimide resin solution. This composite porous membrane had a thickness of 27 μm, an air permeability of 410 cc / 100 cc Air, a shutdown temperature of 121 ° C., and a meltdown temperature of 200 ° C. or higher.

[Example 4]
Using the same apparatus as in Example 1, 0.93 mol of TMA, 0.07 mol of polycaprolactone (Placcel 220: molecular weight 2000, manufactured by Daicel Chemical Industries), 0.5 mol of TODI, 0.3 mol of TDI, diphenylmethane-4,4′-diisocyanate 0 .2 mol and 0.02 mol of potassium fluoride were added together with N-methyl-2-pyrrolidone so that the solid content concentration would be 30%, and after reacting at 150 ° C. for about 5 hours, the solid content concentration would be 20%. Diluted with N-methyl-2-pyrrolidone. The obtained polyamideimide resin had a logarithmic viscosity of 0.71 dl / g and a glass transition temperature of 175 ° C. A composite porous membrane was prepared in the same manner as in Example 1 using a solution in which 20 parts of ethylene glycol was blended with 100 parts of this polyamideimide resin solution. The composite porous membrane had a thickness of 27 μm, an air permeability of 670 sec / 100 cc Air, a shutdown temperature of 121 ° C., and a meltdown temperature of 200 ° C. or higher.

[Example 5]
Using the same apparatus as in Example 1, 0.5 mol of TMA, 0.5 mol of dimer acid, 0.5 mol of TODI, and 0.5 mol of TDI were charged together with N-methyl-2-pyrrolidone so that the solid concentration was 30%. The mixture was reacted at 120 ° C. for 1.5 hours and at 180 ° C. for 3 hours, and then diluted with N-methyl-2-pyrrolidone so that the solid concentration was 20%. The obtained polyamideimide resin had a logarithmic viscosity of 0.70 dl / g and a glass transition temperature of 153 ° C. A composite porous membrane was prepared in the same manner as in Example 1 using a solution in which 20 parts of ethylene glycol was blended with 100 parts of this polyamideimide resin solution. The porous film had a thickness of 28 μm, an air permeability of 4.1 sec / 100 cc Air, a shutdown temperature of 121 ° C., and a meltdown temperature of 186 ° C.

[Example 6]
A solution obtained by blending 20 parts of ethylene glycol with 100 parts of the polyamideimide resin solution of Example 4 was applied to a 100 μm polyester film, immersed in water to solidify, washed with water, and dried to form a polyamideimide porous film having a thickness of 32 μm. Got. This porous membrane had a porosity of 67%, an air permeability of 6.3 sec / 100 cc Air, a shutdown temperature of 178 ° C., and a meltdown temperature of 200 ° C. or higher. Battery performance such as discharge capacity and cycle durability of a coin battery using this polyamideimide porous membrane as a separator in the same configuration as in Example 1 showed the same characteristics as the polyolefin porous membrane single separator.

[Example 7]
Using a solution obtained by blending 20 parts of polyethylene glycol # 400 with 100 parts of the polyamideimide resin solution of Example 5, a 35 μm thick porous polyamideimide film was obtained in the same manner as in Example 6. This porous film had a porosity of 71%, an air permeability of 6.8 sec / 100 cc Air, a shutdown temperature of 151 ° C., and a meltdown temperature of 200 ° C. or higher.

[Example 8]
After immersing a polyolefin porous membrane (25 μm) manufactured by Tonen Chemical in a solution in which 20 parts of polyethylene glycol # 400 was blended with 100 parts of the polyamideimide resin solution of Example 1, the dry film thicknesses were measured on both sides of the polyolefin porous membrane. It is scraped with a squeeze roll so as to be 1 μm, put into a coagulation bath having a water / N-methyl-2-pyrrolidone ratio of 70/30, coagulated, washed and dried to form a composite porous layer having a thickness of 27 μm. A membrane was obtained. The composite porous membrane had a shutdown temperature of 120 ° C. and a meltdown temperature of 200 ° C. or higher. The battery performance such as the discharge capacity and cycle durability of the coin battery prepared by using the composite porous membrane as a separator and having the same structure as in Example 1 showed the same characteristics as the polyolefin porous membrane single separator.

[Example 9]
Discharge capacity and cycle endurance of a coin battery in which a composite membrane obtained by laminating a polyolefin porous membrane on the polyamideimide porous membrane side of the polyamideimide / polyolefin composite porous membrane prepared in Example 1 under the same conditions as in Example 1 The battery performance such as the property showed almost the same characteristics as the polyolefin porous membrane single separator.

[Comparative Example 1]
A polyamideimide resin was synthesized under the same conditions as in Example 1 except that TMA was changed to 1.07 mol in Example 1. The obtained polyamideimide resin had a logarithmic viscosity of 0.35 dl / g and a glass transition temperature of 285 ° C. A porous membrane using this polyamideimide resin is fragile because of its low molecular weight, and is not suitable as a separator.

[Comparative Example 2]
Using the same apparatus as in Example 1, a polyamideimide resin was synthesized under the same conditions as in Example 1 except that the acid component was 0.15 mol of TMA and 0.85 mol of dimer acid. The obtained polyamideimide resin had a logarithmic viscosity of 0.63 dl / g and a glass transition temperature of 55 ° C. Using this polyamideimide resin solution, a porous membrane was prepared in the same manner as in Example 6. The porous film had a thickness of 23 μm, a porosity of 67%, and an air permeability of 3.4 sec / 100 cc Air. The shutdown temperature was 62 ° C. and the meltdown temperature was 118 ° C. Safety was insufficient.

  The present invention provides lithium ion excellent in balance between shutdown characteristics and meltdown characteristics by using a polyamideimide resin porous film having a specific structure or a composite porous film in which a polyamideimide resin porous film and a polyolefin film are laminated. A separator for a secondary battery can be provided.

Claims (7)

The glass transition temperature is 70 ° C. or higher, the logarithmic viscosity is 0.5 dl / g or higher, and is composed of the following structural formulas (I) and (II). The molar ratio of the structural formula (I) to the structural formula (II) is 90/10. The separator for lithium ion secondary batteries which consists of a porous film | membrane with the whole film thickness of 5-100 micrometers containing the polyamideimide resin layer which is the range of-10/90 .

The glass transition temperature is 70 ° C. or higher, the logarithmic viscosity is 0.5 dl / g or higher, and the entire film thickness is 5 to 100 μm, including the polyamideimide resin layer having the following structural formulas (I) and (II) as essential components. A separator for a lithium ion secondary battery comprising a porous membrane, wherein 1 to 60 mol% of an acid component of a polyamideimide resin is dimer acid, polyalkylene ether, polyester, and carboxyl groups, hydroxyl groups, and amino groups at the ends. at least one copolymerized polyamideimide resin der ruri lithium ion secondary battery separator has been replaced by a group consisting of butadiene rubber containing either.

  The separator for a lithium ion secondary battery according to claim 1 or 2, wherein a polyolefin-based porous film is combined with the polyamideimide resin layer in the porous film.   The separator for a lithium ion secondary battery according to any one of claims 1 to 3, which has an air permeability of 1 to 2000 sec / 100 cc Air.   The porous membrane is mixed or mixed with the solvent in which the polyamide-imide resin is dissolved after the polyamide-imide resin solution is applied or immersed in the base material. The separator for lithium ion secondary batteries in any one of Claims 1-4 obtained by making it.   A solution in which the porous membrane is mixed with a solvent in which the polyamideimide resin is dissolved after the polyamideimide resin solution is applied or immersed on one or both surfaces of the polyolefin-based porous membrane, but is a poor solvent for the polyamideimide resin. The separator for a lithium ion secondary battery according to any one of claims 1 to 4, which is obtained by being charged and solidified.   A lithium ion secondary battery comprising the lithium ion secondary battery separator according to claim 1.