JP4625142B2 - Non-aqueous secondary battery adsorbent, non-aqueous secondary battery porous membrane, non-aqueous secondary battery separator and non-aqueous secondary battery - Google Patents

Description

  The present invention relates to an adsorbent for a non-aqueous secondary battery, a porous film for a non-aqueous secondary battery, a separator for a non-aqueous secondary battery, and a non-aqueous secondary battery.

  Non-aqueous secondary batteries represented by lithium ion secondary batteries are widely used as main power sources for portable electronic devices such as mobile phones and notebook computers. This non-aqueous secondary battery is required to have higher energy density, higher capacity, and higher output, and this demand is expected to increase in the future. From the viewpoint of meeting such demands, ensuring the safety of the battery becomes a more important technical element.

  Generally, a non-aqueous secondary battery has a configuration including a positive electrode, a negative electrode, and a separator disposed between these electrodes. The separator has a function of preventing an internal short circuit between the positive electrode and the negative electrode without hindering the permeation of ions. As the separator, a polyolefin microporous membrane is generally used. The separator made of a microporous polyolefin membrane has a shutdown function such that when the battery temperature rises due to overcharge or the like, the polyolefin melts and closes the pores, thereby blocking the current inside the battery. Have. With this function, further heat generation of the battery can be prevented, and the safety of the battery at high temperatures can be improved. However, if the internal temperature of the battery rises even after the holes are closed, there is a risk that the separator will break and an internal short circuit will occur, leading to ignition and the like.

  Therefore, conventionally, heat-resistant porous membranes have attracted attention in order to improve the safety of non-aqueous secondary batteries. According to such a heat-resistant porous film, it is possible to prevent an internal short circuit between the positive and negative electrodes when the battery is exposed to an abnormally high temperature. For example, a technique for applying a porous film made of a heat resistant resin to a separator (Patent Document 1), a technique for applying a porous film made of a heat resistant resin and a ceramic powder to a separator (Patent Documents 2 and 3), an inorganic filler and a binder A technique for forming a porous film made of resin on the electrode surface (Patent Document 4) corresponds to this. A technique for dispersing an inorganic filler in a separator made of a polyolefin microporous film is also known (Patent Document 5). In these techniques, the inorganic filler typified by ceramic powder is considered to be effective from the viewpoint of more reliably preventing internal short circuit between the positive and negative electrodes because of high heat resistance and compressive strength.

  However, a battery to which such an inorganic filler is applied may cause a decrease in battery durability such as cycle characteristics and storage characteristics. As one of the causes of the decrease in durability, hydrogen fluoride (HF) present in a minute amount in the battery reacts with the inorganic filler, and the surface of the inorganic filler is fluorinated, and at this time, water is generated. It is conceivable that moisture decomposes the SEI (Solid Electrolyte Interface) film formed on the electrolyte solution or the electrode surface. If the electrolytic solution or the SEI film is decomposed in this way, the internal resistance of the battery is increased, or lithium necessary for charging / discharging is deactivated, so that the durability of the battery may be reduced. In addition, when such a decomposition reaction occurs, gas is generated, which may also decrease the durability of the battery. And there is a concern that such a decomposition reaction may cause a decrease in battery safety. In particular, when a heat resistant resin such as an aromatic polyamide resin is used together with an inorganic filler, since the heat resistant resin is generally a substance that easily adsorbs moisture, it can be said that the problem of the decomposition reaction is more likely to occur. .

  On the other hand, Patent Document 6 proposes a technique for improving gas generation in a battery with an inorganic filler. In this technique, a gas absorbent made of inorganic powder is mixed in a separator made of polyolefin, and the gas generated in the battery is trapped by the gas absorbent. However, there is a concern that such a separator has insufficient heat resistance. Moreover, since the inorganic filler which is a gas absorbent is mixed in the polyolefin microporous film having the shutdown function, the shutdown function may be remarkably deteriorated. Therefore, although the gas generation is apparently suppressed, the safety of the battery may be reduced as compared with the case where the conventional polyolefin microporous membrane is applied.

  As described above, although there is a demand for higher performance in non-aqueous secondary batteries, it is actually difficult to ensure both safety and durability in order to achieve this. In addition, it is considered effective to apply a porous film made of an inorganic filler and a heat-resistant resin in order to enhance safety, but a configuration that can achieve both safety and durability has not yet been found.

  By the way, in the technical field of separators and porous membranes, the problem of achieving both battery safety and durability has been described above. However, in the first place, from the viewpoint of preventing the deterioration of the durability of the battery due to HF and water existing in the battery, even if it is considered to be extended to the entire technical area of the non-aqueous secondary battery, there has been sufficient improvement technology in the past. Not proposed. This will be described below.

  Generally, a lithium ion secondary battery is composed of a positive electrode such as a lithium transition metal composite oxide, a negative electrode such as a carbon material, an organic electrolytic solution in which a Li salt is dissolved, and a separator such as a polyethylene microporous film. . And such a lithium ion secondary battery is manufactured after strictly managing so that a water | moisture content and an impurity may not mix in a battery system from a viewpoint of cycling characteristics and safety | security. However, it is substantially difficult to completely remove a small amount of moisture adsorbed on the battery constituent member and moisture mixed during battery assembly from the battery system.

Here, moisture present in the battery system reacts with a Li salt such as lithium hexafluorophosphate to liberate HF, and the liberated HF reacts as shown in (1) to (3) below. It is known to deteriorate the cycle characteristics of the battery.
(1) Dissolve the transition metal used in the positive electrode.
(2) When aluminum is used as the positive electrode current collector, the aluminum corrodes.
(3) When graphite is used for the negative electrode, the interface resistance of the negative electrode is increased (see Non-Patent Document 1).

  Therefore, conventionally, as one method for improving the cycle characteristics, a technique for adding a porous inorganic filler such as zeolite, silica gel, activated alumina, activated carbon or the like to the battery system has been reported (see, for example, Patent Documents 7 to 9). ).

That is, Patent Document 7 discloses a technique in which an inorganic substance having a specific surface area of 15 to 300 m ² / g is included in a separator, and it is shown that the cycle characteristics are improved by this inorganic substance. Patent Document 8 discloses a technique in which alumina having a specific surface area of 30 to 300 m ² / g is contained in a negative electrode or a positive electrode, and shows that good cycle characteristics can be obtained. Patent Document 9 discloses a configuration in which activated carbon having a specific surface area of 1000 m ² / g or more and an inorganic substance are included in the battery system, and it is shown that good cycle characteristics can be obtained by activated carbon or the like.

Thus, it has been reported that the porous inorganic filler having a specific specific surface area has an effect of improving the cycle characteristics of the battery.
However, when considering the reaction and adsorption with HF as described in (1) to (3) above, it is considered that there is a range of specific surface areas where good cycle characteristics can be obtained in each adsorbent. It is the current situation that has not been clarified. In addition, a technique for suppressing the reaction with HF and improving the cycle characteristics by factors other than the specific surface area of the inorganic filler is not known.

JP 2008-266588 A Japanese Patent No. 3175730 International Publication No. 2008/62727 Pamphlet JP 2008-204788 A Japanese Patent No. 4074116 JP 2008-146963 A Japanese Patent No. 4145762 Japanese Patent No. 3704780 JP 2000-77103 A

Lithium-ion secondary battery 2nd edition (Nikkan Kogyo Shimbun, Masayuki Yoshio) Materials and Applications Pages 76-77

  Therefore, in view of the above-described problems, the first object of the present invention is to provide a technique capable of improving both safety and durability of a non-aqueous secondary battery. A second object is to provide a technique capable of improving cycle characteristics in consideration of reaction with HF and adsorption.

  As a result of repeated studies to solve the above problems, the present inventors have found that the problems can be solved by the following configuration, and have reached the present invention.

1. An adsorbent of hydrogen fluoride mixed in a non-aqueous secondary battery, wherein the adsorbent has a specific surface area of 300 to 1000 m ² / g and is amorphous activated alumina particles. Adsorbent for non-aqueous secondary battery.
2. 2. The adsorbent for non-aqueous secondary batteries according to 1 above, wherein the active alumina particles have a true density of 2.7 to 3.8 g / cm ³ .
3. 3. The element ratio of O / Al present on the surface of the activated alumina particles is 1.0 to 2.5 when measured using an X-ray photoelectron spectrometer. Adsorbent for non-aqueous secondary batteries.
4). A porous membrane for a non-aqueous secondary battery comprising an inorganic filler and a binder resin,
A porous membrane for a nonaqueous secondary battery, wherein the inorganic filler contains the adsorbent for a nonaqueous secondary battery according to any one of 1 to 3 above.
5. A separator for a non-aqueous secondary battery comprising a porous substrate and a porous layer containing an inorganic filler and a binder resin laminated on one or both surfaces of the porous substrate,
A non-aqueous secondary battery separator comprising the non-aqueous secondary battery adsorbent according to any one of 1 to 3 as the inorganic filler.
6). A non-aqueous secondary battery comprising a positive electrode, a negative electrode, a non-aqueous electrolyte and a separator,
A non-aqueous secondary battery comprising the non-aqueous secondary battery adsorbent according to any one of 1 to 3 in the battery.

  According to the first aspect of the present invention, it is possible to provide a technique capable of improving both safety and durability of a non-aqueous secondary battery. In addition, according to the second aspect of the present invention, it is possible to provide a technique capable of improving cycle characteristics in consideration of reaction with HF and adsorption.

(1) 1st this invention (1-1) 1st form [porous film for non-aqueous secondary batteries]
The porous membrane for a non-aqueous secondary battery according to the first aspect of the present invention is a porous membrane for a non-aqueous secondary battery configured to contain a heat-resistant resin and an inorganic filler, and the inorganic filler has an average particle size It is a porous filler having a diameter of 0.1 to 5.0 μm and a specific surface area of 40 to 3000 m ² / g.

By including a heat-resistant resin and an inorganic filler as in the present invention, it becomes possible to ensure sufficient heat resistance to prevent an internal short circuit even when the battery is exposed to high temperatures, thereby improving the safety of the battery. It can be secured. In addition, since the inorganic filler is a porous filler having an average particle diameter of 0.1 to 5.0 μm and a specific surface area of 40 to 3000 m ² / g, side reactions that reduce durability in the battery are performed. By suppressing or removing the gas generated by the side reaction, durability such as battery cycle characteristics and storage characteristics can be improved.

In particular, since the heat-resistant resin is generally a substance that easily adsorbs moisture, the present invention has a configuration in which the side reaction between the HF and the inorganic filler is likely to occur. By applying the filler, the activity of moisture and HF present in a minute amount in the battery can be significantly reduced, and gas generation due to decomposition of the electrolyte and the like can be suppressed. Even if gas is generated, the porous filler can trap this gas. For this reason, it becomes possible to significantly improve the durability of the battery.
Here, the porous membrane for a battery according to the present invention includes a heat-resistant resin and an inorganic filler, and has a plurality of pores or voids therein, and these pores are connected to each other. Means a quality structure.

  The heat-resistant resin in the present invention includes a resin having a melting point of 200 ° C. or higher. In addition to a resin having a melting point of 200 ° C. or higher, a resin having a thermal decomposition temperature of 200 ° C. or higher with substantially no melting point. Is also included. Examples of such a heat-resistant resin include wholly aromatic polyamides, polyimides, polyamideimides, polysulfones, polyketones, polyether ketones, polyether sulfones, polyether imides, celluloses, combinations of two or more thereof, and the like. . Among them, wholly aromatic polyamides are preferable from the viewpoint of durability such as ease of forming a porous structure, binding property with an inorganic filler, strength of the porous film and accompanying oxidation resistance. As for the wholly aromatic polyamide, comparing the para type and the meta type, the meta type wholly aromatic polyamide is preferable from the viewpoint of easy molding, and polymetaphenylene isophthalamide is particularly preferable.

When the meta type wholly aromatic polyamide is applied, when the meta type wholly aromatic polyamide is dissolved in N-methyl-2-pyrrolidone, the logarithmic viscosity of the following formula (1) is 0.8 to 2.5 dl / g. Those within the range are preferable, and those within the range of 1.0 to 2.2 dl / g are more preferable. Deviating from this range is not preferable because the moldability may be deteriorated.
Logarithmic viscosity (unit: dl / g) = ln (T / T0) / C (1)
T: Flow time of capillary viscometer at 30 ° C. in solution of 0.5 g of meta-type wholly aromatic polyamide resin in 100 ml of N-methyl-2-pyrrolidone T0: Capillary viscosity at 30 ° C. of N-methyl-2-pyrrolidone Total flow time C: Concentration of meta-type wholly aromatic polyamide resin in solution (g / dl)

Porous fillers applicable to the present invention include zeolite, activated carbon, activated alumina, porous silica, porous fillers obtained by heat treatment of metal hydroxides such as magnesium hydroxide and aluminum hydroxide, synthesized from organic compounds Porous fillers to be used. Of these, activated alumina is particularly preferable. The activated alumina in the present invention is a porous filler whose formula is represented by Al ₂ O ₃ × xH ₂ O (x can take a value of 0 or more and 3 or less). The surface of the activated alumina is amorphous Al ₂ O ₃ , γ-Al ₂ O ₃ , χ-Al ₂ O ₃ , gibbsite-like Al (OH) ₃ , boehmite-like Al ₂ O ₃ .H ₂ O, etc. It is preferable to have a structure, and it is particularly preferable that the porous structure is formed of these surface structures from the viewpoint of reducing the activity of moisture and HF. In addition to the porous filler described above, other non-porous inorganic fillers such as metal oxides such as α-alumina and metal hydroxides such as aluminum hydroxide may be appropriately added as the inorganic filler.

  The porous filler is preferably composed of mesopores of 50 nm or less or micropores of 2 nm or less, and particularly preferably has a structure in which micropores of 2 nm or less are developed from the viewpoint of manifestation of the effects of the present invention. .

  The average particle size of the porous filler is preferably in the range of 0.1 to 5.0 μm. When the average particle size of the porous filler is smaller than 0.1 μm, it is not preferable because it may be difficult to mold the porous film, or the sliding property of the porous film may be deteriorated and handling may be difficult. When the average particle diameter of the porous filler is larger than 5.0 μm, it may be difficult to form the porous film from the viewpoint of surface roughness when it is thinly formed.

In the present invention, the specific surface area of the porous filler is preferably 40 to 3000 m ² / g. If the specific surface area is less than 40 m ² / g, the activity of moisture and HF cannot be sufficiently lowered, which is not preferable. On the other hand, when it exceeds 3000 m ² / g, it becomes difficult to mold the porous membrane, and the strength of the porous membrane may be significantly reduced. In such a case, handling may be hindered, which is not preferable.

When the specific surface area of the porous filler is verified in more detail from the viewpoint of the effect of the present invention, the specific surface area of the porous filler is more preferably 40 to 1000 m ² / g. This is because if the specific surface area is 1000 m ² / g or less, the mechanical strength and gas generation suppression are further improved. More preferably, the specific surface area of the porous filler is preferably 40 to 500 m ² / g. This is because if the specific surface area is 500 m ² / g or less, the mechanical strength and the suppression of gas generation become better. The specific surface area of the porous filler is particularly preferably 150 to 500 m ² / g. This is because if the specific surface area is 150 m ² / g or more, it becomes more excellent in terms of suppressing gas generation. Here, the specific surface area is obtained by analyzing the adsorption isotherm measured by the nitrogen gas adsorption method using the BET equation.

In particular, in the present invention, the porous filler is preferably activated alumina having a specific surface area of 300 to 1000 m ² / g. Such activated alumina can reduce the activity of HF by adsorbing or reacting with a small amount of HF generated in the battery, and can further improve the cycle characteristics of the non-aqueous secondary battery. .

  The O / Al element ratio present on the surface of the activated alumina particles is preferably 1.0 to 2.5 when measured using an X-ray photoelectron spectrometer. More preferably, the O / Al element ratio is 1.2 to 1.8. When the surface is formed with such an element ratio, it is preferable from the viewpoint of reducing the activity of HF or the like.

True density of the active alumina is preferably 2.7~3.8g / cm ^3, still more preferably from 2.8~3.3g / cm ^3. When the true density is less than 2.7 g / cm ³ , it becomes close to aluminum hydroxide or the like, and it is difficult to obtain the effect of reducing the activity of HF. On the other hand, if the true density is larger than 3.8 g / cm ³ , the structure of the filler becomes dense, the gap through which the electrolytic solution enters becomes small, and the cycle characteristics of the battery may be deteriorated.

The specific surface area of the activated alumina is preferably 300 m ² / g or more. If the specific surface area is less than 300 m ² / g, the activity of HF or the like may not be sufficiently reduced. On the other hand, the specific surface area of the activated alumina is preferably 1000 m ² / g or less, more preferably 500 m ² / g or less. At present, it is technically difficult to obtain activated alumina having a specific surface area exceeding 1000 m ² / g.

The porous membrane for a non-aqueous secondary battery of the present invention can be applied to any part as long as it is disposed between both the positive electrode and the negative electrode.
That is, for example, the porous membrane for a non-aqueous secondary battery of the present invention can be applied as a separator disposed between electrodes. In this case, it is preferable that the puncture strength has a sufficient mechanical strength of 200 g or more. Further, those having a Gurley value of 10 to 300 seconds / 100 cc are preferred. In order to obtain such physical properties, the porous membrane for a battery according to the present invention preferably has a porous filler weight of 10 to 50% by weight based on the total weight of the heat resistant resin and the porous filler. . If the weight of the porous filler exceeds 50% by weight, it may be difficult to obtain sufficient mechanical strength. On the other hand, if the weight of the porous filler is less than 10% by weight, the effect of suppressing side reactions in the battery may be reduced, or the permeability may be lowered.

  Moreover, when arrange | positioning between the electrodes as a separator for battery porous films of this invention, you may use this porous film for batteries independently. Moreover, in order to add a shutdown function, it may be laminated with a polyolefin microporous film having this function, or a dispersion liquid comprising polyolefin fine particles may be applied to the battery porous film.

  Further, the battery porous membrane of the present invention may be directly formed on the electrode. In this case, since the electrode becomes a support having sufficient strength, mechanical strength is not required as compared with the case where the porous membrane for a battery is applied alone as a separator. From such a viewpoint, the weight of the porous filler is preferably 10 to 90% by weight, and more preferably 50 to 90% by weight with respect to the total weight of the heat resistant resin and the porous filler. If the weight of the porous filler is less than 10% by weight, the effect of suppressing side reactions in the battery may be reduced, which is not preferable. Moreover, since it may become difficult to shape | mold when it exceeds 90 weight%, it is not preferable.

  As described above, when the battery porous membrane of the present invention is directly formed on the electrode, the battery porous membrane can also serve as a separator. Therefore, a separator for preventing a short circuit between the positive and negative electrodes is not disposed. Also good. In addition to the porous membrane for a battery of the present invention, a battery may be produced by applying only a normal separator such as a polyolefin microporous membrane. In addition, when forming the porous membrane for batteries of this invention directly on an electrode, you may apply to any of a positive electrode and a negative electrode. However, it is preferable to form the positive electrode from the viewpoint of improving the durability of the battery, and it is more preferable to form the positive electrode and the negative electrode.

[Method for producing porous membrane for battery]
Although the manufacturing method of the porous film for non-aqueous secondary batteries of this invention is not specifically limited, For example, it can manufacture with the manufacturing method containing the process of the following (i)-(iv). That is, (i) a step of producing a coating slurry containing a heat resistant resin, an inorganic filler and a water-soluble organic solvent, (ii) a step of coating the obtained coating slurry on a support, and (iii) And (iv) a step of coagulating the heat resistant resin in the coated slurry, and (iv) a step of washing and drying the sheet after the coagulation step.

  In the step (i), the water-soluble organic solvent is not particularly limited as long as it is a good solvent for the heat-resistant resin. Specific examples of such a water-soluble organic solvent include polar solvents such as N-methylpyrrolidone, dimethylacetamide, dimethylformamide, and dimethylsulfoxide. Further, in the slurry, a solvent that becomes a poor solvent for the heat-resistant resin can be partially mixed and used. By applying such a poor solvent, a microphase separation structure is induced and the formation of a heat-resistant porous layer is facilitated. As the poor solvent, alcohols are preferred, and polyhydric alcohols such as glycol are particularly preferred.

In the step (ii), the amount of slurry applied to the support is preferably about 10 to 60 g / m ² . Examples of the coating method include a knife coater method, a gravure coater method, a screen printing method, a Mayer bar method, a die coater method, a reverse roll coater method, an ink jet method, a spray method, and a roll coater method. Among them, the reverse roll coater method is preferable from the viewpoint of uniformly applying the coating film.

  In the step (iii), as a method of solidifying the heat-resistant resin in the slurry, a method of spraying a coagulation liquid onto the support after coating or a bath containing the coagulation liquid (coagulation bath) Examples include a method of immersing the substrate. The coagulation liquid is not particularly limited as long as it can coagulate the heat-resistant resin, but water or a mixed liquid in which an appropriate amount of water is contained in a good solvent used in the slurry is preferable. Here, the mixing amount of water is preferably 40 to 80% by weight with respect to the coagulation liquid.

  In the step (iv), the drying method is not particularly limited, but the drying temperature is suitably 50 to 100 ° C. In the case of applying a high drying temperature, it is preferable to apply a method of contacting the roll in order to prevent dimensional change due to heat shrinkage.

  Moreover, as a second production method for obtaining the porous membrane for a non-aqueous secondary battery of the present invention, for example, (v) the coated sheet is dried after the steps (i) and (ii). It is also possible to carry out the process. In this case, the drying temperature in the above step (v) may be any temperature as long as the water-soluble solvent can be removed, but approximately 50 to 200 ° C. is appropriate. In the case of applying a high drying temperature, it is preferable to apply a method of contacting the roll in order to prevent dimensional change due to heat shrinkage.

  In any of the above production methods, a support is used, and as this support, a glass plate, a film made of polyethylene terephthalate (PET), or the like that exhibits sufficient heat resistance against the drying temperature is suitable. Can be used. In addition, when applying these supports, a step of peeling the porous membrane for a battery of the present invention from the support after the drying of (iv) and (v) above is included.

  In the present invention, it is also possible to apply a porous material such as a polyolefin microporous film or a nonwoven fabric to the support. In this case, since it can be applied as a porous film for a battery including a support, a peeling step is unnecessary. It is also possible to apply the electrode to the support and directly form the battery porous membrane of the present invention on the electrode. Also in this case, the peeling step is naturally unnecessary.

[Non-aqueous secondary battery]
The non-aqueous secondary battery of the present invention is a non-aqueous secondary battery including at least a positive electrode and a negative electrode, and the porous film for a non-aqueous secondary battery described above is provided on at least one surface of the positive electrode and the negative electrode. The porous film for non-aqueous secondary batteries is used as a separator.

  The non-aqueous secondary battery of the present invention is improved in battery safety by applying a battery porous film excellent in heat resistance, and the generation of gas is suppressed by the porous filler in the battery porous film. It also has excellent durability such as characteristics and storage characteristics.

  As described above, the battery porous membrane of the present invention may be applied as a separator or may be formed on the electrode surface. When applied as a separator, only the porous film for a battery may be applied alone, or the porous film for a battery may be laminated with a polyolefin microporous film. When the porous membrane for a battery is formed on the electrode surface, it may be formed on either the positive electrode or the negative electrode, or both. When the battery porous membrane is formed on the electrode surface, a polyolefin microporous membrane or the like may be applied as a separator, or the battery porous membrane of the present invention is formed in advance on the electrode surface, so that no separator is used. The positive electrode and the negative electrode may be joined together.

  However, when a polyolefin microporous membrane is applied to the separator, a configuration in which the battery porous membrane of the present invention is at least between the polyolefin microporous membrane and the positive electrode is preferable. The oxidation resistance of polyolefin microporous membranes is not necessarily sufficient for application to non-aqueous secondary batteries. Polyolefin microporous membranes may oxidize the surface in contact with the positive electrode, which may deteriorate the battery. By disposing the porous membrane for a battery of the invention as described above, this deterioration can be greatly suppressed.

  The type and configuration of the non-aqueous secondary battery of the present invention is not limited to the above configuration, but the battery element in which the positive electrode, the separator, and the negative electrode are sequentially laminated is impregnated with the electrolyte, and this is enclosed in the exterior Any structure can be applied as long as the structure is the same. However, as described above, the separator can be omitted.

  The negative electrode has a structure in which a negative electrode mixture composed of a negative electrode active material, a conductive additive and a binder is formed on a current collector. As the current collector, for example, copper foil, stainless steel foil, nickel foil or the like is used. As the negative electrode active material, a material capable of electrochemically doping lithium, for example, a carbon material, silicon, aluminum, tin, or the like is used.

The positive electrode has a structure in which a positive electrode mixture composed of a positive electrode active material, a conductive additive and a binder is formed on a current collector. As the current collector, for example, copper foil, stainless steel foil, nickel foil or the like is used. Examples of the positive electrode active material include lithium-containing transition metal oxides such as LiCoO ₂ , LiNiO ₂ , LiMn _0.5 Ni _0.5 O ₂ , LiCo _1/3 Ni _1/3 Mn _1/3 O ₂ , LiMn ₂ O. ₄ and LiFePO ₄ are used.

The electrolytic solution has a structure in which a lithium salt is dissolved in a non-aqueous solvent. Examples of the lithium salt include LiPF ₆ , LiBF ₄ , LiClO _{4, and the} like. Examples of the non-aqueous solvent include propylene carbonate, ethylene carbonate, dimethyl carbonate, diethyl carbonate, ethyl methyl carbonate, γ-butyrolactone, vinylene carbonate, and the like.

  Examples of the exterior material include a metal can or an aluminum laminate pack. The shape of the battery includes a square shape, a cylindrical shape, a coin shape, and the like, but the separator of the present invention can be suitably applied to any shape. However, when the battery porous membrane of the present invention is formed on an electrode, it is more preferable to apply to a cylindrical battery.

(1-2) Second Embodiment The porous membrane for a non-aqueous secondary battery according to the second embodiment of the present invention is a porous membrane for a non-aqueous secondary battery configured to contain a heat resistant resin and an inorganic filler. The inorganic filler is amorphous alumina particles (hereinafter referred to as amorphous alumina as appropriate).

  According to the present invention as described above, the same effects as those of the first embodiment described above can be obtained. In particular, since amorphous alumina adsorbs a small amount of impurities and by-products such as HF present in the battery, the cycle characteristics of the battery can be further improved.

In addition, since this 2nd form is the same as the 1st form mentioned above except the point which changed the inorganic filler into the amorphous alumina, below, description is abbreviate | omitted suitably about the structure similar to a 1st form. To do. In addition, the “amorphous alumina” in the second form has an effect similar to that of the “active alumina having a specific surface area of 300 to 1000 m ² / g” in the first form described above. What caught the invention from the viewpoint corresponds to the first form, and what caught from the viewpoint of the crystal structure corresponds to the second form.

In the present invention, amorphous alumina particles are fillers whose formula is expressed by Al ₂ O ₃ .xH ₂ O (x can take a value of 0 or more and 3 or less), and X-rays A clear crystal peak is not confirmed by analysis by diffraction. In addition, amorphous alumina does not have a clear crystal peak completely confirmed by X-ray diffraction analysis, but has a slightly clear crystal peak in a broad peak (amorphous and other compositions). And mixed composition).

The “other composition” includes gibbsite or bayerite Al (OH) ₃ , boehmite or diaspore Al ₂ O ₃ .H ₂ O, γ-Al ₂ O ₃ or χ-Al ₂ O _3. transition alumina etc., and contains α-Al ₂ O ₃ is corundum, in that the effect of the present invention among these obtained good boehmite or gibbsite is preferable.

The “slightly clear crystal peak” is observed, for example, in the vicinity of 2θ = 14 ° when measured under the conditions described in the examples described later, when an amorphous alumina contains a boehmite structure as an example. If the integrated intensity of the main peak is 10 cps · deg or more and this integrated intensity is 0.30 or less with respect to the integrated intensity of the broad peak existing over 2θ = 10-60 deg, the entire inorganic filler Can be said to be amorphous. Further, for example, in the case of the gibbsite structure, 2θ = 18 °, in the case of the bayerite structure, in the vicinity of 2θ = 19 °, in the case of the diaspore structure, in the vicinity of 2θ = 20 °, and in the case of the γ-Al ₂ O ₃ structure, 2θ = 46. The integrated intensity of the main peak observed is around 2θ = 10 ° in the vicinity of °, 2θ = 67 ° in the case of the χ-Al ₂ O ₃ structure, and 2θ = 43 ° in the case of the α-Al ₂ O ₃ structure. Even when the integrated intensity of the broad peak existing over 60 deg is 0.30 or less, the whole inorganic filler can be said to be amorphous.

  The O / Al element ratio present on the surface of the amorphous alumina is preferably 1.0 to 2.5 when measured using an X-ray photoelectron spectrometer. More preferably, the O / Al element ratio is 1.2 to 1.8. When the surface is formed with such an element ratio, it is preferable from the viewpoint of reducing the activity of hydrogen fluoride (HF) or the like in the battery.

  The amorphous alumina preferably has a porous structure with a large adsorption area for adsorbing various impurities and by-products mixed in the battery system. The porous structure referred to here means a structure in which a large number of micropores or microvoids are formed inside or on the surface of the particle.

  The amorphous alumina is preferably configured to include mesopores of 50 nm or less or micropores of 2 nm or less, and in particular, from the viewpoint of manifesting the effects of the present invention, the structure has developed micropores of 2 nm or less. preferable.

The specific surface area of the amorphous alumina is preferably 50 m ² / g or more. When the specific surface area is less than 50 m ² / g, deterioration of cycle characteristics due to moisture, impurities, or the like cannot be sufficiently suppressed. On the other hand, the specific surface area of amorphous alumina is preferably 1000 m ² / g or less, more preferably 500 m ² / g or less. At present, it is technically difficult to obtain activated alumina having a specific surface area exceeding 1000 m ² / g.

The average particle diameter of the amorphous alumina is preferably in the range of 0.1 to 5.0 μm. If the average particle diameter of the amorphous alumina is smaller than 0.1 μm, it is not preferable because it may be difficult to mold the porous film, or the sliding property of the porous film may be deteriorated and handling may be difficult. Moreover, when the average particle diameter of amorphous alumina is larger than 5.0 μm, it may be difficult to form the porous film from the viewpoint of surface roughness when it is thinly formed, which is not preferable.
The amorphous alumina may be used by mixing other inorganic fillers such as metal oxides such as α-alumina and metal hydroxides such as aluminum hydroxide.

(1-3) Third embodiment [Separator for non-aqueous secondary battery]
The separator for a non-aqueous secondary battery according to the third aspect of the present invention is a heat-resistant porous material including a porous substrate and a heat-resistant resin and an inorganic filler laminated on one or both surfaces of the porous substrate. A separator for a non-aqueous secondary battery, wherein the inorganic filler has an average particle size of 0.1 to 5.0 μm and a specific surface area of 40 to 3000 m ² / g. It is a filler.

By including a heat-resistant resin and an inorganic filler as in the present invention, it becomes possible to ensure sufficient heat resistance to prevent an internal short circuit even when the battery is exposed to high temperatures, thereby improving the safety of the battery. Can be secured. Moreover, since it is the structure which forms a heat resistant porous layer in a porous base material, it becomes easy to ensure sufficient mechanical strength as a separator. And since an inorganic filler is a porous filler with an average particle diameter of 0.1-5.0 micrometers and a specific surface area of 40-3000 m < ² > / g, the side reaction which reduces durability in a battery is carried out. By suppressing or removing the gas generated by the side reaction, durability such as battery cycle characteristics and storage characteristics can be improved.

  In addition, since this 3rd form is the structure which formed the porous film for batteries in the 1st form mentioned above as a heat resistant porous layer on the porous base material, in the following, the 1st form The description of the same configuration as that of the embodiment is omitted as appropriate.

  In the present invention, the porous substrate is not particularly limited as long as it has a large number of pores or voids inside and has a porous structure in which these pores are connected to each other. Examples thereof include a microporous membrane, a nonwoven fabric, a paper-like sheet, and other sheets having a three-dimensional network structure. Among these, a microporous membrane is preferable from the viewpoint of handling properties and strength. As the material constituting the porous substrate, both organic materials and inorganic materials can be used, but thermoplastic resins such as polyolefins are preferable from the viewpoint of obtaining shutdown characteristics. Therefore, if such a polyolefin porous substrate is applied, both heat resistance and a shutdown function can be achieved.

  Examples of the polyolefin resin include polyethylene, polypropylene, polymethylpentene, and the like. Among them, those containing 90% by weight or more of polyethylene are preferable from the viewpoint of obtaining good shutdown characteristics. As the polyethylene, for example, low density polyethylene, high density polyethylene, ultrahigh molecular weight polyethylene and the like are preferably used, and particularly, high density polyethylene and ultra high molecular weight polyethylene are suitable. Furthermore, polyethylene comprising a mixture of high density polyethylene and ultra high molecular weight polyethylene is preferred from the viewpoint of strength and moldability. The molecular weight of polyethylene is preferably 100,000 to 10,000,000 in terms of weight average molecular weight, and particularly preferably a polyethylene composition containing at least 1% by weight of ultrahigh molecular weight polyethylene having a weight average molecular weight of 1,000,000 or more. In addition, the porous substrate in the present invention may be constituted by mixing other polyolefins such as polypropylene and polymethylpentene in addition to polyethylene, or two or more layers of a polyethylene microporous membrane and a polypropylene microporous membrane. You may comprise as a laminated body of.

  In the present invention, the film thickness of the porous substrate is not necessarily limited, but a range of about 5 to 20 μm is preferable. If the film thickness is less than 5 μm, sufficient strength cannot be obtained, handling becomes difficult, and the yield of the battery may be significantly reduced. When the film thickness is larger than 20 μm, it is not preferable because the movement of ions becomes difficult or the volume occupied by the separator in the battery increases and the energy density of the battery may be lowered.

  The porosity of the porous substrate is preferably 10 to 60%, more preferably 20 to 50%. When the porosity is lower than 10%, it is difficult to maintain an amount of electrolyte sufficient for battery operation, and the charge / discharge characteristics of the battery may be significantly deteriorated. If the porosity exceeds 60%, the shutdown characteristics may be insufficient or the strength may be lowered, which is not preferable.

  The puncture strength of the porous substrate is preferably 200 g or more, more preferably 250 g or more, more preferably 300 g or more. If the piercing strength is lower than 200 g, the strength for preventing a short circuit between the positive and negative electrodes of the battery is not sufficient, and there may be a problem that the manufacturing yield does not increase.

  The Gurley value (JIS P8117) of the porous substrate is preferably in the range of 100 to 500 seconds / 100 cc, more preferably in the range of 100 to 300 seconds / 100 cc. When the Gurley value is lower than 100 seconds / 100 cc, although ion permeability is excellent, shutdown characteristics and mechanical strength may be deteriorated, which is not preferable. On the other hand, if the Gurley value is larger than 500 seconds / 100 cc, the ion permeability becomes insufficient and the load characteristics of the battery may be deteriorated, which is not preferable.

  The average pore size of the porous substrate is preferably 10 to 100 nm. If the average pore diameter is smaller than 10 nm, it may be difficult to impregnate the electrolytic solution, which is not preferable. When the average pore diameter is larger than 100 nm, the interface may be clogged when the heat-resistant porous layer is formed, or the shutdown characteristics may be significantly deteriorated when the porous layer is formed. .

  The heat-resistant porous layer in the present invention includes a heat-resistant resin and an inorganic filler, and has a porous structure in which a large number of pores or voids are formed inside and these pores are connected to each other. It has become. Such a heat-resistant porous layer is preferably an embodiment in which the inorganic filler is directly fixed on the porous substrate in a state where the inorganic filler is dispersed and bound in the heat-resistant resin, from the viewpoint of handling properties and the like. It should be noted that a porous layer made of only a heat resistant resin is formed on a porous substrate, and a solution containing an inorganic filler is subsequently applied and immersed in the hole or surface of the heat resistant resin layer. The aspect which the inorganic filler adhered may be sufficient. Further, the heat-resistant porous layer may be configured as an independent porous sheet such as a microporous film, a nonwoven fabric, or a paper-like sheet, and the porous sheet may be adhered to the porous substrate. Good.

  The separator for a non-aqueous secondary battery of the present invention is characterized in that the above-mentioned inorganic filler is contained in the heat-resistant porous layer, but the inorganic filler is not contained in the porous substrate. Is one of the features. The function of the inorganic filler can be expected to be expressed even if it is not present in the porous layer. For example, even if the inorganic filler is contained in the porous substrate, the effect of suppressing gas generation can be obtained. . However, such a configuration is not preferable because, when a polyolefin porous substrate is applied, the shutdown function may be significantly impaired. For this reason, it is preferable in terms of construction that an inorganic filler is not contained in a layer that is expected to have a shutdown function but is contained in a porous layer that is expected to have heat resistance.

  The composition of the porous layer is preferably in the range of heat-resistant resin: inorganic filler = 10: 90 to 80:20, and more preferably in the range of 10:90 to 50:50, by weight ratio. When the content of the inorganic filler is less than 20% by weight, it may be difficult to sufficiently obtain the characteristics of the inorganic filler, which is not preferable. If the content of the inorganic filler exceeds 90% by weight, it may be difficult to mold, which is not preferable. On the other hand, those containing 50% by weight or more of the inorganic filler are preferable because heat resistance characteristics such as an effect of suppressing thermal shrinkage are improved.

  The porosity of the heat resistant porous layer is preferably in the range of 30 to 80%. Furthermore, the porosity of the heat resistant porous layer is preferably higher than the porosity of the porous substrate. Such a configuration has advantages in characteristics such as better ion permeability and good shutdown characteristics.

  When the heat resistant porous layer is formed on both surfaces of the porous substrate, the total thickness of the heat resistant porous layer is preferably 2 μm or more and 12 μm or less. When the porous porous layer is formed only on one side, it is preferably 2 μm or more and 12 μm or less.

  The nonaqueous secondary battery separator of the present invention preferably has a thickness of 7 to 25 μm, more preferably 10 to 20 μm. If the film thickness is thinner than 7 μm, it is not preferable from the viewpoint of mechanical strength. Further, if it exceeds 25 μm, it is not preferable from the viewpoint of ion permeability, and it is also not preferable from the viewpoint that the volume occupied by the separator in the battery is increased and the energy density is lowered.

  The porosity of the separator for nonaqueous secondary batteries of the present invention is preferably 20 to 70%, more preferably 30 to 60%. If the porosity is lower than 20%, it may be difficult to hold a sufficient amount of electrolyte for battery operation, which is not preferable. If the porosity exceeds 70%, the shutdown characteristics may be insufficient, and the strength and heat resistance may be lowered.

  The puncture strength of the separator for a non-aqueous secondary battery of the present invention is preferably 200 g or more, more preferably 250 g or more, and further preferably 300 g or more. If the piercing strength is lower than 200 g, the strength for preventing a short circuit between the positive and negative electrodes of the battery is not sufficient, which may cause a problem that the production yield does not increase, which is not preferable.

  The Gurley value (JIS P8117) in the nonaqueous secondary battery separator of the present invention is preferably in the range of 150 to 600 seconds / 100 cc, more preferably in the range of 150 to 400 seconds / 100 cc. When the Gurley value is lower than 150 seconds / 100 cc, although ion permeability is excellent, shutdown characteristics and mechanical strength may be deteriorated, which is not preferable. Further, when forming the porous layer, there is a possibility that a problem such as clogging may occur at the interface between the porous substrate and the heat-resistant porous layer. When the Gurley value is larger than 600 seconds / 100 cc, the ion permeability becomes insufficient and the load characteristics of the battery may be deteriorated.

  The value obtained by subtracting the Gurley value of the porous substrate applied to the Gurley value of the separator for a non-aqueous secondary battery of the present invention is preferably 250 seconds / 100 cc or less, and more preferably 200 seconds / 100 cc or less. . A smaller value is preferable in terms of characteristics such as better shutdown characteristics and improved ion permeability.

  In the present invention, the heat-resistant porous layer may be formed on at least one surface of the porous substrate, but it is more preferable to form it on both the front and back surfaces of the porous substrate. By forming a heat-resistant porous layer on both the front and back sides of the porous substrate, the handling properties are improved without curling, the heat resistance such as dimensional stability at high temperatures is improved, and the cycle characteristics of the battery are also significantly improved. The effect is obtained.

[Method for producing separator for non-aqueous secondary battery]
Although the manufacturing method of the separator for non-aqueous secondary batteries of this invention is not specifically limited, For example, it can manufacture with the manufacturing method containing the process of the following (i)-(iv). (I) a step of preparing a slurry for coating containing a heat-resistant resin, an inorganic filler, and a water-soluble organic solvent; and (ii) coating the obtained coating slurry on one or both sides of a porous substrate. And (iii) a step of coagulating the heat resistant resin in the coated slurry, and (iv) a step of washing and drying the sheet after the coagulation step. . In addition, these processes (i)-(iv) are the same as that of the case of the 1st form mentioned above.

  In the present invention, the method for producing the porous substrate is not particularly limited. For example, a polyolefin microporous film as a porous substrate can be produced as follows. That is, a gel-like mixture of polyolefin and liquid paraffin is extruded from a die and then cooled to produce a base tape, which is stretched and heat-set. Thereafter, liquid paraffin is extracted by immersing it in an extraction solvent such as methylene chloride, and then the extraction solvent is dried to obtain a polyolefin microporous membrane.

[Non-aqueous secondary battery]
The nonaqueous secondary battery according to the third aspect of the present invention is a nonaqueous secondary battery including a positive electrode, a negative electrode, and a separator, and the separator for a nonaqueous secondary battery described above is used as the separator. It is characterized by. Such a non-aqueous secondary battery is excellent in safety and durability at high temperatures, and is excellent in cycle characteristics and the like. Other battery configurations are the same as those in the first embodiment described above.

(1-4) Fourth Embodiment A non-aqueous secondary battery separator according to a fourth embodiment of the present invention is a porous substrate and a heat resistant resin laminated on one or both sides of the porous substrate. And a heat-resistant porous layer containing an inorganic filler, wherein the inorganic filler is amorphous alumina particles.

According to the present invention as described above, the same effects as those of the third embodiment described above can be obtained. In particular, since amorphous alumina adsorbs a small amount of impurities and by-products such as HF present in the battery, the cycle characteristics of the battery can be further improved.
In addition, since this 4th form is the same as the 3rd form mentioned above except the point which changed the inorganic filler into the amorphous alumina, description is abbreviate | omitted about the structure similar to a 3rd form.

(2) Second invention The first invention described above is a configuration that solves the problem of compatibility between battery safety and durability in the technical field of separators and the like. The configuration using “300 to 1000 m ² / g of activated alumina” or “amorphous alumina” is excellent in improving the cycle characteristics of the battery because the activity of HF is significantly reduced. Therefore, in the second aspect of the present invention, focusing on this action effect, “active alumina” and “amorphous alumina” are regarded as hydrogen fluoride adsorbents, and this adsorbent is applied to each part of a non-aqueous secondary battery. explain.

(2-1) Fifth Embodiment An adsorbent for a non-aqueous secondary battery according to a fifth embodiment of the present invention is an adsorbent for hydrogen fluoride mixed in the non-aqueous secondary battery, and the adsorbent. Is characterized by being activated alumina particles having a specific surface area of 300 to 1000 m ² / g.

In the present invention, activated alumina having a specific surface area of 300 to 1000 m ² / g is used as the adsorbent for non-aqueous secondary batteries, so that this activated alumina adsorbs or reacts with HF generated in a trace amount in the battery. Thus, the activity of HF can be reduced, and the cycle characteristics of the nonaqueous secondary battery can be improved. Conventionally, there has been a technique in which only the specific surface area is specified without specifying the type of porous filler, but the present invention is from the aspect that activated alumina having a specific surface area decreases the activity of HF. The present invention has been made by finding that it exhibits excellent cycle characteristics different from other porous inorganic fillers. The details of why activated alumina is superior are not known. However, as one of the reasons, since alumina is an amphoteric oxide known as a Lewis acid / Lewis base, it can be considered that HF was polarized and HF was trapped efficiently. Moreover, it is thought that by making the specific surface area 300 m ² / g or more, the surface reaction was performed smoothly and the cycle characteristics were improved. At present, it is technically difficult to obtain activated alumina having a specific surface area exceeding 1000 m ² / g.

The configuration of the “activated alumina particles having a specific surface area of 300 to 1000 m ² / g” in the fifth embodiment is the same as that in the first embodiment described above, and thus the description thereof is omitted.

[Location of activated alumina]
The following (A)-(C) are mentioned as an aspect containing the said activated alumina.
(A) A porous membrane for a non-aqueous secondary battery comprising an inorganic filler and a binder resin, wherein the activated alumina is contained as the inorganic filler. film.
(B) A separator for a non-aqueous secondary battery comprising a porous substrate and a porous layer containing an inorganic filler and a binder resin laminated on one or both surfaces of the porous substrate, A separator for a non-aqueous secondary battery, wherein the activated alumina is contained as an inorganic filler.
(C) A nonaqueous secondary battery comprising a positive electrode, a negative electrode, a nonaqueous electrolyte, and a separator, wherein the activated alumina is contained in the battery.

  As shown in the above (A) to (C), the activated alumina may be contained in a separator, may be contained in a porous film laminated on a separator or an electrode, or contained in a positive electrode and a negative electrode. In addition, you may make it contain in electrolyte solution. However, when mixed with the electrode mixture, the volume of the active material is reduced correspondingly, and the battery capacity is impaired. Therefore, an embodiment in which activated alumina is contained in the separator is preferable. Furthermore, in order to achieve both the shutdown function and the heat resistance function, the surface of the porous substrate made of a thermoplastic resin such as polyethylene is coated with a heat resistant porous layer made of a heat resistant resin such as polyamide, An embodiment in which activated alumina is contained in the heat resistant porous layer is preferred.

  When the active alumina is included in the positive electrode, the positive electrode active material, the binder, and the conductive agent in the first embodiment described above and the active alumina are uniformly mixed to produce a positive electrode mixture. Disperse in a solvent to make a positive electrode mixture slurry. Next, the positive electrode mixture is applied to the positive electrode current collector by, for example, a doctor blade method. Subsequently, the positive electrode containing activated alumina is obtained by drying at high temperature to volatilize the solvent and pressurizing. In addition, the active alumina is fixed on the positive electrode by coating the active material side of the positive electrode with a coating solution in which the active alumina is dispersed in a solvent such as NMP without containing the active alumina in the positive electrode mixture and drying. Is also effective.

  When the negative electrode contains the activated alumina, the negative electrode active material, the binder, and the conductive agent in the first embodiment described above and the active alumina are uniformly mixed to prepare a negative electrode mixture. Disperse in a solvent to make a negative electrode mixture slurry. Then, after applying this negative electrode mixture to the negative electrode current collector in the same manner as the positive electrode, the negative electrode containing activated alumina is obtained by drying at high temperature to volatilize and pressurize the solvent. In addition, the active alumina is fixed on the negative electrode by coating the active material side of the negative electrode with a coating solution in which the active alumina is dispersed in a solvent such as NMP without containing the active alumina in the negative electrode mixture. Is also effective.

  When the separator contains the activated alumina, for example, after adding the activated alumina to a thermoplastic resin such as polyethylene, the step of melt-kneading to prepare a thermoplastic resin solution containing the activated alumina, this solution from the die Extruding and cooling to form a gel-like molded product, a primary stretching step and a secondary stretching step, a step of removing the liquid solvent from the gel-shaped molded product, and a step of drying the obtained film, A separator can be obtained as a thermoplastic resin microporous film containing activated alumina. In addition, for example, a coating solution in which a binder resin such as aromatic polyamide and activated alumina are uniformly dispersed is applied on a base film such as a polypropylene film, solidified, washed and dried, and then the coating film is peeled off. Can also be obtained.

  In the case of a laminated separator, activated alumina may be contained in any one of the layers, or in all layers. For example, when a coating liquid in which a heat-resistant resin such as aromatic polyamide and activated alumina are uniformly dispersed is coated on one or both surfaces of a porous substrate such as a polyethylene microporous film or nonwoven fabric, a laminated separator containing activated alumina Is obtained. In addition, for example, a porous substrate such as a nonwoven fabric is immersed in a coating solution in which a binder resin such as PVdF and activated alumina is uniformly dispersed, taken out, and then washed and dried to obtain a composite separator. It can also be obtained.

  In the separator and porous membrane described above, the binder resin for binding the activated alumina is not only a heat-resistant resin such as aromatic polyamide, but also a thermoplastic such as polyvinylidene fluoride (PVdF), PVdF copolymer, and polyethylene. Examples thereof include resins. Since the configurations of the heat-resistant resin, the porous substrate, the electrode in the non-aqueous secondary battery, the electrolytic solution, the exterior material, and the like are described in detail in the first embodiment described above, the description thereof is omitted.

(2-2) Sixth embodiment The non-aqueous secondary battery adsorbent according to the sixth embodiment of the present invention is an adsorbent of hydrogen fluoride mixed in the non-aqueous secondary battery, and the adsorbent Is characterized by amorphous alumina particles.
In the present invention, since amorphous alumina is used as the adsorbent for non-aqueous secondary batteries, amorphous alumina adsorbs minute impurities generated in the battery and by-products such as HF. Cycle characteristics can be improved.

In addition, since this 6th form is the same as that of the 5th form mentioned above except the point which changed the adsorbent into amorphous alumina, description is abbreviate | omitted about the structure similar to the 5th form mentioned above. In addition, as described above, “activated alumina having a specific surface area of 300 to 1000 m ² / g” and “amorphous alumina” have functions and effects that are very similar to each other. In view of the crystal structure, amorphous alumina is used. As an aspect containing the said amorphous alumina, it is the same as that of the aspect of (A)-(C) in the 5th form mentioned above. Furthermore, the amorphous alumina is preferably contained in any part between the positive electrode and the negative electrode in order to suppress internal short circuit.

(1) Reference examples according to first and second embodiments Hereinafter, reference examples according to the first and second embodiments of the present invention will be described. The measurement method applied in this reference example is as follows.

[Average particle size of inorganic filler]
It measured with the laser diffraction type particle size distribution measuring apparatus (Shimadzu Corporation make; SALD-2000J). Water was used as a dispersion medium, and a small amount of nonionic surfactant “Triton X-100” was used as a dispersant. The center particle diameter (D50) in the obtained volume particle size distribution was defined as the average particle diameter.

[Specific surface area of inorganic filler]
Measurement was performed according to JIS K 8830. Using NOVA-1200 (manufactured by Yuasa Ionics Co., Ltd.), the BET equation was used for analysis and determination by the nitrogen gas adsorption method. The sample weight at the time of measurement was 0.1 to 0.2 g. The analysis was performed by a three-point method, and the specific surface area was obtained from the BET plot.

[Analysis of crystal structure of inorganic filler]
As for the crystal structure of the inorganic filler, the XRD diffraction spectrum of the inorganic filler was measured with a powder X-ray diffractometer, and the crystal structure in the bulk structure was analyzed from this spectrum. As the X-ray diffractometer, an X-ray generator ultrax 18 manufactured by Rigaku was used, and Cu-Kα rays were used. The measurement conditions were 45 KV-60 mA, sampling interval 0.020 °, measurement range (2θ) 5 ° to 90 °, and scan speed 5 ° / min. As the measurement sample, an agate mortar was used to pulverize the inorganic filler manually and packed into a glass sample plate. The glass sample plate has a groove having a length of 18 mm, a width of 20 mm, and a depth of 0.2 mm, and the thickness of the sample is the depth of the glass sample plate.

[Measurement of element ratio of inorganic filler]
The elemental ratio of O / Al present on the surface of the inorganic filler was measured using an X-ray photoelectron spectrometer (manufactured by VG, ESCALAB200), and calculated from the obtained O1s and Al2p intensity ratio. MgKα ray was used as the X-ray source.

[Film thickness]
It was determined by measuring 20 points with a contact-type film thickness meter (manufactured by Mitutoyo Co., Ltd.) and averaging them. Here, the contact terminal was a cylindrical one having a bottom surface of 0.5 cm in diameter.

[Reference Example 1-1]
Aluminum hydroxide (manufactured by Showa Denko; H-43M) was heat-treated at 280 ° C. to obtain activated alumina having an average particle diameter of 0.8 μm and a specific surface area of 400 m ² / g. When an XRD analysis was performed on this activated alumina, a peak derived from boehmite was observed in a broad chart, and the integrated intensity of the peak at 2θ = 14.39 ° was 98 cps · deg. The integrated intensity of the peak was 0.07 with respect to the integrated intensity of the broad peak existing over 2θ = 10 to 60 deg. Therefore, this activated alumina can be said to be amorphous alumina because it mainly has an amorphous bulk structure and a very small amount of boehmite phase is mixed. The elemental ratio of O / Al on the surface of this activated alumina was 1.54.
Conex (registered trademark; manufactured by Teijin Techno Products), which is polymetaphenylene isophthalamide, was used as the meta-type wholly aromatic polyamide. A Conex solution was prepared by dissolving so that Conex was 7% by weight in a weight ratio of dimethylacetamide (DMAc): tripropylene glycol (TPG) = 60: 40.
The activated alumina was dispersed in the Conex solution so that the activated alumina: Conex = 30: 70 (weight ratio) to prepare a slurry.
The slurry was applied to a glass plate, and this was immersed in a coagulating liquid having a weight ratio of water: DMAc: TPG = 70: 18: 12 (weight ratio) of 30 ° C., then washed with water and dried. It was. And the porous film formed on the glass plate was peeled, and the 10-micrometer-thick porous film with sufficient handling property was obtained.

[Reference Example 1-2]
Except for changing the activated alumina to a zeolite (HSZ-341NHA; manufactured by Tosoh Corporation) having an average particle diameter of 4 μm and a specific surface area of 700 m ² / g, the film thickness is 10 μm with a sufficient handling property by the same method as Reference Example 1-1 A porous membrane was obtained.

[Reference Example 1-3]
By performing wet pulverization (2 mm zirconia bead mill) using dimethylacetamide (DMAc) as a dispersion solvent on activated carbon (manufactured by Kansai Thermal Chemical Co., Ltd .; MSP-20), the average particle size is 0.6 μm and the specific surface area is 1600 m ^2. / G of activated carbon was obtained.
A porous film having a thickness of 10 μm was obtained in the same manner as in Reference Example 1-1 except that the activated alumina was changed to the activated carbon. In addition, this porous film was a little weak compared with the thing of the reference example 1-1, and was inferior to handling property.

[Reference Example 1-4]
A porous film having a thickness of 10 μm was obtained in the same manner as in Reference Example 1-1 except that the weight ratio of activated alumina to Conex was changed to activated alumina: Conex = 70: 30 (weight ratio). This porous film was slightly brittle and inferior in handling property as compared with that of Reference Example 1-1.

[Reference Example 1-5]
The porous membrane for batteries produced in Reference Example 1-1 was coated with a polyethylene aqueous dispersion (Kemipearl W900: manufactured by Mitsui Chemicals) and dried to obtain a porous membrane having a thickness of 13 μm.

[Reference Comparative Example 1-1]
Handling with a film thickness of 10 μm in the same manner as in Reference Example 1-1 except that the activated alumina was changed to aluminum hydroxide (Showa Denko; H-43M) having an average particle diameter of 0.8 μm and a specific surface area of 8 m ² / g. A porous film having sufficient properties was obtained.

[Reference Comparative Example 1-2]
Handling ability with a film thickness of 10 μm is the same as in Reference Example 1-1 except that the activated alumina is changed to alumina having an average particle diameter of 0.6 μm and a specific surface area of 6 m ² / g (Showa Denko: AL160SG-3). A sufficient porous membrane was obtained.

[Reference Comparative Example 1-3]
Conex (registered trademark; manufactured by Teijin Techno Products), which is polymetaphenylene isophthalamide, was used as the meta-type wholly aromatic polyamide. A Conex solution was prepared by dissolving so that Conex was 7% by weight in a weight ratio of dimethylacetamide (DMAc): tripropylene glycol (TPG) = 60: 40.
The Conex solution was applied to a glass plate, and this was immersed in a coagulating liquid having a weight ratio of water: DMAc: TPG = 70: 18: 12 (weight ratio) of 30 ° C., then washed with water and dried. Went. And the porous film formed on the glass plate was peeled, and the 10-micrometer-thick porous film with sufficient handling property was obtained.

[Reference Comparative Example 1-4]
As polyethylene powder, GUR2126 (weight average molecular weight 41.50 million, melting point 141 ° C.) and GRX143 (weight average molecular weight 560,000, melting point 135 ° C.) manufactured by Ticona were used. The liquid paraffin (manufactured by Matsumura Oil Research Co., Ltd .; Smoyl P-350P; boiling point 480 ° C.) and decalin so that GUR2126 and GURX143 are 1: 9 (weight ratio) and the polyethylene concentration is 15% by weight. A polyethylene solution was prepared by dissolving in a mixed solvent. The composition of the polyethylene solution is polyethylene: liquid paraffin: decalin = 30: 45: 25 (weight ratio).
A slurry in which zeolite (HSZ-500KOA; manufactured by Tosoh Corporation) was dispersed in the polyethylene solution was prepared. Here, the mixing ratio of polyethylene and zeolite was 50:50 by weight. The zeolite had an average particle size of 3 μm and a specific surface area of 290 m ² / g.
This slurry was extruded from a die at 148 ° C. and cooled in a water bath to prepare a gel tape (base tape). The base tape was dried at 60 ° C. for 8 minutes and at 95 ° C. for 15 minutes, and the base tape was biaxially stretched by successively performing longitudinal stretching and transverse stretching. Here, the longitudinal stretching was performed at a stretching ratio of 5.5 times and a stretching temperature of 90 ° C., the transverse stretching was performed at a stretching ratio of 11.0 times, and the stretching temperature was 105 ° C. After stretching, heat setting was performed at 125 ° C. Next, this was immersed in a methylene chloride bath to extract liquid paraffin and decalin. Thereafter, the film was dried at 50 ° C. and annealed at 120 ° C. to obtain a porous film with sufficient handling property of 10 μm.

[Reference Comparative Example 1-5]
Aluminum hydroxide (Showa Denko; H-43M) was heat-treated at 205 ° C. to obtain activated alumina having an average particle diameter of 0.8 μm and a specific surface area of 30 m ² / g. As a result of structural analysis of this activated alumina by XRD, a broad peak derived from the amorphous structure was not confirmed, and a peak derived from the gibbsite was clearly observed, so that the bulk structure was mainly gibbsite and amorphous. It turned out not to be alumina.
A porous membrane having a handleability of 10 μm in thickness was obtained in the same manner as in Reference Example 1-1 except that this activated alumina was used instead of the activated alumina in Reference Example 1-1.

[Bearing test]
For each of the porous membranes of Reference Examples 1-1 to 1-5 and Reference Comparative Examples 1-1 to 1-5 produced as described above, a membrane breaking test was performed as follows. First, the porous film of the sample was fixed to a metal frame having a length of 6.5 cm and a width of 4.5 cm. The temperature of the oven was set to 175 ° C., and the sample fixed to the metal frame was put in the oven and held for 1 hour. At this time, a film that was not broken and the shape could be maintained was evaluated as ◯, and a film that was not evaluated as X. The results are shown in Table 1.

[Gas generation test]
For each of the porous membranes of Reference Examples 1-1 to 1-5 and Reference Comparative Examples 1-1 to 1-5 produced as described above, a membrane breaking test was performed as follows. First, each porous membrane used as a sample was cut into a size of 240 cm ² and vacuum-dried at 85 ° C. for 16 hours. This was put in an aluminum pack in an environment with a dew point of −60 ° C. or less, an electrolyte was further injected, and the aluminum pack was sealed with a vacuum sealer to produce a measurement cell. Here, the electrolytic solution was 1M LiPF ₆ ethylene carbonate (EC) / ethyl methyl carbonate (EMC) = 3/7 (weight ratio) (manufactured by Kishida Chemical Co., Ltd.). The measurement cell was stored at 85 ° C. for 3 days, and the volume of the measurement cell before and after storage was measured. A value obtained by subtracting the volume of the measurement cell before storage from the volume of the measurement cell after storage was taken as the gas generation amount. Here, the volume measurement of the measurement cell was performed at 23 ° C., and was performed using an electronic hydrometer (manufactured by Alpha Mirage Co., Ltd .; EW-300SG) according to Archimedes' principle. The results are shown in Table 1.

[Production of non-aqueous secondary battery]
Using each of the porous membranes of Reference Examples 1-1 to 1-5 and Reference Comparative Examples 1-1 to 1-5 produced as described above, non-aqueous secondary batteries were produced as follows.
89.5 parts by weight of lithium cobalt oxide (LiCoO ₂ ; manufactured by Nippon Chemical Industry Co., Ltd.), 4.5 parts by weight of acetylene black (manufactured by Denki Kagaku Co., Ltd .; trade name Denka Black), 6 polyvinylidene fluoride (manufactured by Kureha Chemical Co., Ltd.) 6 These were kneaded using an N-methyl-2pyrrolidone solvent so as to be parts by weight to prepare a slurry. The obtained slurry was applied onto an aluminum foil having a thickness of 20 μm, dried and pressed to obtain a positive electrode having a thickness of 100 μm.
87 parts by weight of mesophase carbon microbeads (MCMB: Osaka Gas Chemical Co., Ltd.) powder, 3 parts by weight of acetylene black (manufactured by Denki Kagaku Kogyo; trade name Denka Black), 10 parts by weight of polyvinylidene fluoride (manufactured by Kureha Chemical Co., Ltd.) Thus, these were knead | mixed using the N-methyl-2 pyrrolidone solvent, and the slurry was produced. The obtained slurry was applied onto a copper foil having a thickness of 18 μm, dried and pressed to obtain a negative electrode having a thickness of 90 μm.

The positive electrode and the negative electrode were opposed to each other through a separator. This was impregnated with an electrolytic solution and sealed in an exterior made of an aluminum laminate film to produce a non-aqueous secondary battery. Here, 1M LiPF ₆ ethylene carbonate / ethyl methyl carbonate (3/7 weight ratio) (manufactured by Kishida Chemical Co., Ltd.) was used as the electrolytic solution.
Here, the porous films of Reference Examples 1-1 to 1-5 and Reference Comparative Examples 1-1 to 1-5 were used as separators, respectively, and Reference Examples 1-6 to 1-10 and Reference Comparison shown in Table 2, respectively. Nonaqueous secondary batteries of Examples 1-6 to 1-10 were produced. The porous films of Reference Examples 1-3 and 1-4 were used by being laminated with a polyethylene microporous film (PE microporous film). The PE microporous film used here was produced by the following method.

First, as the polyethylene powder, GUR2126 (weight average molecular weight 4150,000, melting point 141 ° C.) and GURX143 (weight average molecular weight 560,000, melting point 135 ° C.) manufactured by Ticona were used. Liquid paraffin (manufactured by Matsumura Oil Research Co., Ltd .; Smoyl P-350P; boiling point 480 ° C.) and decalin so that GUR2126 and GURX143 are 1: 9 (weight ratio) and the polyethylene concentration is 30% by weight. A polyethylene solution was prepared by dissolving in a mixed solvent. The composition of the polyethylene solution is polyethylene: liquid paraffin: decalin = 30: 45: 25 (weight ratio).
This polyethylene solution was extruded from a die at 148 ° C. and cooled in a water bath to prepare a gel tape (base tape). The base tape was dried at 60 ° C. for 8 minutes and at 95 ° C. for 15 minutes, and the base tape was biaxially stretched by successively performing longitudinal stretching and transverse stretching. Here, the longitudinal stretching was performed at a stretching ratio of 5.5 times and a stretching temperature of 90 ° C., the transverse stretching was performed at a stretching ratio of 11.0 times, and the stretching temperature was 105 ° C. After stretching, heat setting was performed at 125 ° C. Next, this was immersed in a methylene chloride bath to extract liquid paraffin and decalin. Then, it dried at 50 degreeC and annealed at 120 degreeC, and obtained the polyethylene microporous film | membrane with a film thickness of 9 micrometers.

[Oven test]
Each battery produced as described above was charged with constant voltage / constant current charging of 0.2 C and 4.2 V for 8 hours. It was put in an oven with a load of 1.8 kg / cm ² applied thereto, heated from 30 ° C. to 150 ° C. at a heating rate of 5 ° C./min, and held at 150 ° C. for 1 hour. At this time, the smoked product was evaluated as x, and the smoked product was evaluated as o. The results are shown in Table 2.

[Cycle characteristics]
The cycle characteristics of each battery produced as described above were evaluated. Evaluation of cycle characteristics is 1C 4.2V 2 hours constant current / constant voltage charge, 1C, charge / discharge with constant current discharge of 2.75V cutoff, 300 cycles when the first cycle capacity is used as a reference The eye capacity retention rate was used as an index of cycle characteristics. The temperature at the time of measurement was 30 ° C. The results are shown in Table 2.

[Save test]
The battery produced as described above was charged for 8 hours at a constant voltage / constant current charge of 0.2 C, 4.2 V. It was put in an oven with a load of 1.8 kg / cm ² applied and stored at 85 ° C. for 3 days. After storage, a constant current discharge of 0.2 C and 2.75 V cut-off was performed to determine the remaining capacity. The capacity retention rate was calculated by multiplying the value obtained by dividing the remaining capacity by the initial capacity by 100. This capacity maintenance rate was used as an index for evaluating the storage test. The results are shown in Table 2.

[Battery swelling]
Each battery after the above storage test was visually confirmed. If the battery was clearly swollen, it was judged as x. If the battery was not clearly swollen, it was judged as yes. In this case, the swelling of the battery is due to the generation of gas in the battery. The results are shown in Table 2.

[Reference Example 1-11]
89.5 parts by weight of lithium cobalt oxide (LiCoO ₂ ; manufactured by Nippon Chemical Industry Co., Ltd.), 4.5 parts by weight of acetylene black (manufactured by Denki Kagaku Co., Ltd .; trade name Denka Black), 6 polyvinylidene fluoride (manufactured by Kureha Chemical Co., Ltd.) 6 These were kneaded using an N-methyl-2pyrrolidone solvent so as to be parts by weight to prepare a slurry. The obtained slurry was applied onto an aluminum foil having a thickness of 20 μm, dried and pressed to obtain a positive electrode having a thickness of 100 μm.
The slurry prepared in Reference Example 1-4 was applied to the surface of the positive electrode, and this was mixed in a coagulating liquid having a weight ratio of water: DMAc: TPG = 70: 18: 12 (weight ratio) of 30 ° C. Immersion was performed, followed by washing with water and drying to form a porous film for a battery having a thickness of 3 μm on the surface of the positive electrode.
87 parts by weight of mesophase carbon microbeads (MCMB: Osaka Gas Chemical Co., Ltd.) powder, 3 parts by weight of acetylene black (manufactured by Denki Kagaku Kogyo; trade name Denka Black), 10 parts by weight of polyvinylidene fluoride (manufactured by Kureha Chemical Co., Ltd.) Thus, these were knead | mixed using the N-methyl-2 pyrrolidone solvent, and the slurry was produced. The obtained slurry was applied onto a copper foil having a thickness of 18 μm, dried and pressed to obtain a negative electrode having a thickness of 90 μm.
The positive electrode and the negative electrode were opposed to each other through a separator. This was impregnated with an electrolytic solution and sealed in an exterior made of an aluminum laminate film to produce a non-aqueous secondary battery. Here, 1M LiPF ₆ ethylene carbonate / ethyl methyl carbonate (3/7 weight ratio) (manufactured by Kishida Chemical Co., Ltd.) was used as the electrolytic solution. The separator used was the PE microporous membrane in Reference Examples 1-8 and 1-9 described above.
The battery of Reference Example 1-11 was also evaluated for the oven test, cycle characteristics, storage test, and battery blistering described above. The results are shown in Table 3.

[Reference Example 1-12]
89.5 parts by weight of lithium cobalt oxide (LiCoO ₂ ; manufactured by Nippon Chemical Industry Co., Ltd.), 4.5 parts by weight of acetylene black (manufactured by Denki Kagaku Co., Ltd .; trade name Denka Black), 6 polyvinylidene fluoride (manufactured by Kureha Chemical Co., Ltd.) 6 These were kneaded using an N-methyl-2pyrrolidone solvent so as to be parts by weight to prepare a slurry. The obtained slurry was applied onto an aluminum foil having a thickness of 20 μm, dried and pressed to obtain a positive electrode having a thickness of 100 μm.
87 parts by weight of mesophase carbon microbeads (MCMB: Osaka Gas Chemical Co., Ltd.) powder, 3 parts by weight of acetylene black (manufactured by Denki Kagaku Kogyo; trade name Denka Black), 10 parts by weight of polyvinylidene fluoride (manufactured by Kureha Chemical Co., Ltd.) Thus, these were knead | mixed using the N-methyl-2 pyrrolidone solvent, and the slurry was produced. The obtained slurry was applied onto a copper foil having a thickness of 18 μm, dried and pressed to obtain a negative electrode having a thickness of 90 μm.
The slurry produced in Reference Example 1-4 was applied to the surface of the negative electrode, and this was mixed in a coagulating liquid having a weight ratio of water: DMAc: TPG = 70: 18: 12 (weight ratio) of 30 ° C. Immersion was then performed, followed by washing with water and drying to form a battery porous film having a thickness of 3 μm on the negative electrode surface.
The positive electrode and the negative electrode were opposed to each other through a separator. This was impregnated with an electrolytic solution and sealed in an exterior made of an aluminum laminate film to produce a non-aqueous secondary battery. Here, 1M LiPF ₆ ethylene carbonate / ethyl methyl carbonate (3/7 weight ratio) (manufactured by Kishida Chemical Co., Ltd.) was used as the electrolytic solution. The separator used was the PE microporous membrane in Reference Examples 1-8 and 1-9 described above.
The battery of Reference Example 1-12 was also evaluated for the oven test, cycle characteristics, storage test, and battery blistering described above. The results are shown in Table 3.

[Reference Example 1-13]
89.5 parts by weight of lithium cobalt oxide (LiCoO ₂ ; manufactured by Nippon Chemical Industry Co., Ltd.), 4.5 parts by weight of acetylene black (manufactured by Denki Kagaku Co., Ltd .; trade name Denka Black), 6 polyvinylidene fluoride (manufactured by Kureha Chemical Co., Ltd.) 6 These were kneaded using an N-methyl-2pyrrolidone solvent so as to be parts by weight to prepare a slurry. The obtained slurry was applied onto an aluminum foil having a thickness of 20 μm, dried and pressed to obtain a positive electrode having a thickness of 100 μm.
87 parts by weight of mesophase carbon microbeads (MCMB: Osaka Gas Chemical Co., Ltd.) powder, 3 parts by weight of acetylene black (manufactured by Denki Kagaku Kogyo; trade name Denka Black), 10 parts by weight of polyvinylidene fluoride (manufactured by Kureha Chemical Co., Ltd.) Thus, these were knead | mixed using the N-methyl-2 pyrrolidone solvent, and the slurry was produced. The obtained slurry was applied onto a copper foil having a thickness of 18 μm, dried and pressed to obtain a negative electrode having a thickness of 90 μm.
The slurry prepared in Reference Example 1-4 was applied to the positive electrode and negative electrode surfaces described above, and this was a coagulating liquid having a weight ratio of water: DMAc: TPG = 70: 18: 12 (weight ratio) of 30 ° C. It was dipped in, then washed with water and dried to form a porous membrane for a battery having a thickness of 3 μm on the positive electrode and negative electrode surfaces.
The positive electrode and the negative electrode were opposed to each other through a separator. This was impregnated with an electrolytic solution and sealed in an exterior made of an aluminum laminate film to produce a non-aqueous secondary battery. Here, 1M LiPF ₆ ethylene carbonate / ethyl methyl carbonate (3/7 weight ratio) (manufactured by Kishida Chemical Co., Ltd.) was used as the electrolytic solution. The separator used was the PE microporous membrane in Reference Examples 1-8 and 1-9 described above.
The battery of Reference Example 1-13 was also evaluated for the oven test, cycle characteristics, storage test, and battery blistering described above. The results are shown in Table 3.

(2) Reference examples according to third and fourth embodiments Hereinafter, reference examples according to the third and fourth embodiments of the present invention will be described. The measurement method applied in this reference example is as follows. In addition, about the average particle diameter of an inorganic filler, a specific surface area, a crystal structure and element ratio, and the measuring method of a film thickness, it is the same as that of the case of the reference example which concerns on the 1st, 2nd form mentioned above. The separator film breakage test and gas generation amount test are the same as those in the reference examples according to the first and second embodiments described above.

[Porosity]
About the film | membrane used as a sample, the weight (Wi: g / m < ² >) of each component material is divided by the true density (di: g / cm < ³ >), and these sums (Σ (Wi / di)) are calculated | required. The porosity (%) was calculated by dividing this by the film thickness (μm) and multiplying the value subtracted from 1 by 100.

[Gurley value]
It measured according to JIS P8117.

[Puncture strength]
Using a KES-G5 handy compression tester manufactured by Kato Tech Co., Ltd., a piercing test was performed under the conditions of a radius of curvature of the needle tip of 0.5 mm and a piercing speed of 2 mm / second, and the maximum piercing load was defined as the piercing strength. Here, the sample was sandwiched and fixed in a metal frame (sample holder) having a hole of Φ11.3 mm.

[Shutdown characteristics (SD characteristics)]
First, a separator as a sample is punched out to a diameter of 19 mm, dipped in a 3 wt% methanol solution of a nonionic surfactant (manufactured by Kao Corporation; Emulgen 210P), and air-dried. Then, the separator was impregnated with the electrolytic solution and sandwiched between SUS plates (Φ15.5 mm). Here, 1 M LiBF ₄ propylene carbonate / ethylene carbonate (1/1 weight ratio) was used as the electrolytic solution. This was enclosed in a 2032 type coin cell. I took the lead from the coin cell, put a thermocouple, and put it in the oven. The cell resistance was measured by raising the temperature at a rate of temperature increase of 1.6 ° C./min and simultaneously applying alternating current with an amplitude of 10 mV and a frequency of 1 kHz.
In the above measurement, when the resistance value was 10 ³ ohm · cm ² or more in the range of 135 to 150 ° C., the SD characteristic was evaluated as “good”, and otherwise, the SD characteristic was evaluated as “poor”.

[Battery storage characteristics]
Using the separators produced in the following examples and comparative examples, non-aqueous secondary batteries were produced as follows.
89.5 parts by weight of lithium cobalt oxide (LiCoO ₂ ; manufactured by Nippon Chemical Industry Co., Ltd.), 4.5 parts by weight of acetylene black (manufactured by Denki Kagaku Co., Ltd .; trade name Denka Black), 6 polyvinylidene fluoride (manufactured by Kureha Chemical Co., Ltd.) 6 These were kneaded using an N-methyl-2pyrrolidone solvent so as to be parts by weight to prepare a slurry. The obtained slurry was applied onto an aluminum foil having a thickness of 20 μm, dried and pressed to obtain a positive electrode having a thickness of 100 μm.
87 parts by weight of mesophase carbon microbeads (MCMB: Osaka Gas Chemical Co., Ltd.) powder, 3 parts by weight of acetylene black (manufactured by Denki Kagaku Kogyo; trade name Denka Black), 10 parts by weight of polyvinylidene fluoride (manufactured by Kureha Chemical Co., Ltd.) Thus, these were knead | mixed using the N-methyl-2 pyrrolidone solvent, and the slurry was produced. The obtained slurry was applied onto a copper foil having a thickness of 18 μm, dried and pressed to obtain a negative electrode having a thickness of 90 μm.

The positive electrode and the negative electrode were opposed to each other through the separators prepared in the following examples and comparative examples. This was impregnated with an electrolytic solution and sealed in an exterior made of an aluminum laminate film to produce a non-aqueous secondary battery. Here, 1M LiPF ₆ ethylene carbonate / ethyl methyl carbonate (3/7 weight ratio) (manufactured by Kishida Chemical Co., Ltd.) was used as the electrolytic solution.
The non-aqueous secondary battery was subjected to constant current / constant voltage charging at 0.2 C 4.2 V for 8 hours and constant current discharge at 0.2 C, 2.75 V cutoff. The discharge capacity obtained at the fifth cycle was defined as the initial capacity of this cell. Then, constant current / constant voltage charging of 0.2C 4.2V for 8 hours was performed, and stored at 85 ° C. for 3 days. And the constant current discharge of 0.2C and 2.75V cut-off was performed, and the residual capacity in storage at 85 ° C. for 3 days was determined. A value obtained by dividing the remaining capacity by the initial capacity and multiplying by 100 was defined as a capacity retention rate, and this capacity retention rate was used as an index of storage characteristics of the battery.

[Battery swelling]
Each battery after the above storage characteristics test of the battery was visually checked. If the battery was clearly swollen, it was judged as x. If the battery was not swollen in appearance, it was judged as yes. . In this case, the swelling of the battery is due to the generation of gas in the battery.

[Reference Example 2-1]
As polyethylene powder, GUR2126 (weight average molecular weight 41.50 million, melting point 141 ° C.) and GRX143 (weight average molecular weight 560,000, melting point 135 ° C.) manufactured by Ticona were used. Liquid paraffin (manufactured by Matsumura Oil Research Co., Ltd .; Smoyl P-350P; boiling point 480 ° C.) and decalin so that GUR2126 and GURX143 are 1: 9 (weight ratio) and the polyethylene concentration is 30% by weight. A polyethylene solution was prepared by dissolving in a mixed solvent. The composition of the polyethylene solution is polyethylene: liquid paraffin: decalin = 30: 45: 25 (weight ratio).
This polyethylene solution was extruded from a die at 148 ° C. and cooled in a water bath to prepare a gel tape (base tape). The base tape was dried at 60 ° C. for 8 minutes and at 95 ° C. for 15 minutes, and the base tape was biaxially stretched by successively performing longitudinal stretching and transverse stretching. Here, the longitudinal stretching was performed at a stretching ratio of 5.5 times and a stretching temperature of 90 ° C., the transverse stretching was performed at a stretching ratio of 11.0 times, and the stretching temperature was 105 ° C. After stretching, heat setting was performed at 125 ° C. Next, this was immersed in a methylene chloride bath to extract liquid paraffin and decalin. Then, it dried at 50 degreeC and obtained the polyethylene microporous film by annealing at 120 degreeC.
The obtained polyethylene microporous membrane had a basis weight of 4.7 g / m ² , a film thickness of 9 μm, a porosity of 45%, a Gurley value of 150 seconds / 100 cc, and a puncture strength of 300 g.
Conex (registered trademark; manufactured by Teijin Techno Products), which is polymetaphenylene isophthalamide, was used as the meta-type wholly aromatic polyamide. Conex solution was prepared by dissolving in 6% by weight of Conex in dimethylacetamide (DMAc): tripropylene glycol (TPG) = 60: 40 (weight ratio).
As the porous filler, zeolite (HSZ-500KOA; manufactured by Tosoh Corporation) having an average particle size of 3 μm and a specific surface area of 290 m ² / g was used. The zeolite was dispersed in the Conex solution so that the ratio of zeolite: Conex = 50: 50 (weight ratio) was obtained to prepare a dispersion.
Two Meyer bars were placed opposite to each other, and an appropriate amount of the dispersion was put between them. The polyethylene microporous membrane was passed between Mayer bars carrying the dispersion, and the dispersion was applied to both sides of the polyethylene microporous membrane. Here, the clearance between the Mayer bars was 30 μm, and the number of the Mayer bars was # 6. This was immersed in a coagulating liquid having a weight ratio of water: DMAc: TPG = 70: 18: 12 (weight ratio) of 30 ° C., then washed with water and dried. A heat resistant porous layer made of Conex was formed to obtain a separator for a non-aqueous secondary battery. The characteristics of the obtained non-aqueous secondary battery separator are shown in Tables 4 and 5. The characteristics of the separators according to the following reference examples and reference comparative examples are also shown in Tables 4 and 5.

[Reference Example 2-2]
A separator for a non-aqueous secondary battery in the same manner as in Reference Example 2-1, except that zeolite (HSZ-980HOA; manufactured by Tosoh Corporation) having an average particle diameter of 2 μm and a specific surface area of 400 m ² / g was used as the porous filler. Got.

[Reference Example 2-3]
A separator for a non-aqueous secondary battery in the same manner as in Reference Example 2-1, except that zeolite (HSZ-341NHA; manufactured by Tosoh Corporation) having an average particle diameter of 4 μm and a specific surface area of 700 m ² / g was used as the porous filler. Got.

[Reference Example 2-4]
Activated carbon (manufactured by Kansai Thermal Chemical Co., Ltd .; MSP-20) is subjected to wet pulverization (2 mm zirconia bead mill) using dimethylacetamide (DMAc) as a dispersion solvent, whereby an average particle diameter of 0.6 μm and a specific surface area of 1600 m ² / g of activated carbon was obtained. A separator for a non-aqueous secondary battery was obtained in the same manner as in Reference Example 2-1, except that this activated carbon was used as a porous filler.

[Reference Example 2-5]
A non-aqueous two-component system was prepared in the same manner as in Reference Example 2-1, except that activated alumina (Sumitomo Chemical Co., Ltd .; KC-501) having an average particle size of 1.4 μm and a specific surface area of 190 m ² / g was used as the porous filler. A separator for a secondary battery was obtained.

[Reference Example 2-6]
Aluminum hydroxide (Showa Denko; H-43M) was heat-treated at 220 ° C. to obtain activated alumina having an average particle diameter of 0.8 μm and a specific surface area of 60 m ² / g. In addition, when the crystal structure of this activated alumina was analyzed by XRD, a broad peak derived from the amorphous structure was not confirmed, and a peak derived from the gibbsite was clearly observed. Therefore, the bulk structure was mainly gibbsite, It turned out not to be alumina.
A separator for a non-aqueous secondary battery was obtained in the same manner as in Reference Example 2-1, except that this activated alumina was used as a porous filler.

[Reference Example 2-7]
Aluminum hydroxide (manufactured by Showa Denko; H-43M) was heat-treated at 280 ° C. to obtain activated alumina having an average particle diameter of 0.8 μm and a specific surface area of 400 m ² / g. When an XRD analysis was performed on this activated alumina, a peak derived from boehmite was observed in a broad chart, and the integrated intensity of the peak at 2θ = 14.39 ° was 98 cps · deg. The integrated intensity of the peak was 0.07 with respect to the integrated intensity of the broad peak existing over 2θ = 10 to 60 deg. Therefore, this activated alumina can be said to be amorphous alumina because it mainly has an amorphous bulk structure and a very small amount of boehmite phase is mixed. The elemental ratio of O / Al on the surface of this activated alumina was 1.54.
A separator for a non-aqueous secondary battery was obtained in the same manner as in Reference Example 2-1, except that this activated alumina was used as a porous filler.

[Reference Example 2-8]
A separator for a non-aqueous secondary battery was obtained in the same manner as in Reference Example 2-7, except that the dispersion was applied to only one surface of a polyethylene microporous membrane to form a porous layer.

[Reference Comparative Example 2-1]
Instead of the porous filler used in Reference Example 2-1, α-alumina (manufactured by Showa Denko: AL160SG-3) having an average particle diameter of 0.6 μm and a specific surface area of 6 m ² / g was applied as an inorganic filler. In the same manner as in Reference Example 2-1, a non-aqueous secondary battery separator was produced.

[Reference Comparative Example 2-2]
Reference Example 2 except that boehmite (Daimei Chemical Co., Ltd .: C06) having an average particle diameter of 0.6 μm and a specific surface area of 15 m ² / g was used as the inorganic filler instead of the porous filler used in Example 1. The separator for non-aqueous secondary batteries was produced like -1.

[Reference Comparative Example 2-3]
Aluminum hydroxide (Showa Denko; H-43M) was heat-treated at 205 ° C. to obtain activated alumina having an average particle diameter of 0.8 μm and a specific surface area of 30 m ² / g. In addition, when the crystal structure of this activated alumina was analyzed by XRD, a broad peak derived from the amorphous structure was not confirmed, and a peak derived from the gibbsite was clearly observed. Therefore, the bulk structure was mainly gibbsite, It turned out not to be alumina. A separator for a non-aqueous secondary battery was obtained in the same manner as in Reference Example 2-1, except that the porous filler was changed to this activated alumina.

[Reference Comparative Example 2-4]
As polyethylene powder, GUR2126 (weight average molecular weight 41.50 million, melting point 141 ° C.) and GRX143 (weight average molecular weight 560,000, melting point 135 ° C.) manufactured by Ticona were used. The liquid paraffin (manufactured by Matsumura Oil Research Co., Ltd .; Smoyl P-350P; boiling point 480 ° C.) and decalin so that GUR2126 and GURX143 are 1: 9 (weight ratio) and the polyethylene concentration is 15% by weight. A polyethylene solution was prepared by dissolving in a mixed solvent. The composition of the polyethylene solution is polyethylene: liquid paraffin: decalin = 30: 45: 25 (weight ratio).
A slurry was prepared by dispersing the polyethylene solution in a weight ratio such that polyethylene: zeolite (HSZ-500KOA; manufactured by Tosoh Corporation) = 50: 50. Here, the zeolite has an average particle diameter of 3 μm and a specific surface area of 290 m ² / g.
This slurry was extruded from a die at 148 ° C. and cooled in a water bath to prepare a gel tape (base tape). The base tape was dried at 60 ° C. for 8 minutes and at 95 ° C. for 15 minutes, and the base tape was biaxially stretched by successively performing longitudinal stretching and transverse stretching. Here, the longitudinal stretching was performed at a stretching ratio of 5.5 times and a stretching temperature of 90 ° C., the transverse stretching was performed at a stretching ratio of 11.0 times, and the stretching temperature was 105 ° C. After stretching, heat setting was performed at 125 ° C. Next, this was immersed in a methylene chloride bath to extract liquid paraffin and decalin. Then, it dried at 50 degreeC and annealed at 120 degreeC, and obtained the polyethylene microporous film (non-aqueous secondary battery separator) containing a porous filler.

[Reference Comparative Example 2-5]
Conex (registered trademark; manufactured by Teijin Techno Products), which is polymetaphenylene isophthalamide, was used as the meta-type wholly aromatic polyamide. Conex solution was prepared by dissolving in 6% by weight of Conex in dimethylacetamide (DMAc): tripropylene glycol (TPG) = 60: 40 (weight ratio).
Two Mayer bars were placed against each other, and an appropriate amount of the Conex solution was placed between them. The polyethylene microporous membrane containing the porous filler prepared in Reference Comparative Example 2-4 was passed between the Mayer bars on which the Conex solution was placed, and the Conex solution was applied to both sides of the polyethylene microporous membrane. Here, the clearance between the Mayer bars was 30 μm, and the number of the Mayer bars was # 6. This is immersed in a coagulating liquid having a weight ratio of water: DMAc: TPG = 70: 18: 12 (weight ratio) of 30 ° C., then washed with water, dried, and a polyethylene microporous film containing a porous filler A porous layer made of Conex was formed on the front and back surfaces of the non-aqueous secondary battery separator.

[Cycle characteristics evaluation]
Next, a non-aqueous secondary battery was manufactured as follows for a separator in which a heat-resistant porous layer was formed on one or both sides of a porous substrate, and it was examined whether there was a difference in cycle characteristics.
89.5 parts by weight of lithium cobalt oxide (LiCoO ₂ ; manufactured by Nippon Chemical Industry Co., Ltd.), 4.5 parts by weight of acetylene black (manufactured by Denki Kagaku Co., Ltd .; trade name Denka Black), 6 polyvinylidene fluoride (manufactured by Kureha Chemical Co., Ltd.) 6 These were kneaded using an N-methyl-2pyrrolidone solvent so as to be parts by weight to prepare a slurry. The obtained slurry was applied onto an aluminum foil having a thickness of 20 μm, dried and pressed to obtain a positive electrode having a thickness of 100 μm.
87 parts by weight of mesophase carbon microbeads (MCMB: Osaka Gas Chemical Co., Ltd.) powder, 3 parts by weight of acetylene black (manufactured by Denki Kagaku Kogyo; trade name Denka Black), 10 parts by weight of polyvinylidene fluoride (manufactured by Kureha Chemical Co., Ltd.) Thus, these were knead | mixed using the N-methyl-2 pyrrolidone solvent, and the slurry was produced. The obtained slurry was applied onto a copper foil having a thickness of 18 μm, dried and pressed to obtain a negative electrode having a thickness of 90 μm.

The positive electrode and the negative electrode were opposed to each other through a separator. This was impregnated with an electrolytic solution and sealed in an exterior made of an aluminum laminate film to produce a non-aqueous secondary battery. Here, 1M LiPF ₆ ethylene carbonate / ethyl methyl carbonate (3/7 weight ratio) (manufactured by Kishida Chemical Co., Ltd.) was used as the electrolytic solution.
Here, the separators of Reference Examples 2-7 and 2-8 were used, and batteries of Reference Examples 2-9 to 2-11 shown in Table 6 were produced.
Evaluation of cycle characteristics is 1C 4.2V 2 hours constant current / constant voltage charge, 1C, charge / discharge with constant current discharge of 2.75V cutoff, 300 cycles when the first cycle capacity is used as a reference The eye capacity retention rate was used as an index of cycle characteristics. The temperature at the time of measurement was 30 ° C. The results are shown in Table 6.

  From the results of Table 6, it was found that the configuration in which the heat-resistant porous layer was formed on both sides of the porous substrate was superior in capacity retention rate than the configuration on one side. It was also found that the capacity retention rate was higher when the polyethylene microporous membrane was arranged on the negative electrode side even with a single-sided configuration.

(3) About the effect of the special activated alumina in a 3rd form Hereinafter, the structure using the activated alumina whose specific surface area is 300-1000 m < ² > / g among the 3rd forms of this invention is examined.
The measurement methods applied in the following reference examples are as follows. In addition, about the measuring method of the average particle diameter of an inorganic filler, a specific surface area, a crystal structure, and element ratio, it is the same as that of the case of the reference example which concerns on the 1st, 2nd aspect mentioned above.

[Measurement of true density of alumina]
About the alumina used by the following reference examples and reference comparative examples, the true density was calculated | required with the micro ultra pycnometer (Yuasa Ionics make MUPY-21T). Helium gas was used for the measurement.

[Reference Example 3-1]
(i) Production of PE Microporous Membrane GUR2126 (weight average molecular weight 4150,000, melting point 141 ° C.) and GURX143 (weight average molecular weight 560,000, melting point 135 ° C.) manufactured by Ticona were used as polyethylene powder. GUR2126 and GURX143 are made to be 1: 9 (weight ratio), and liquid paraffin (manufactured by Matsumura Oil Research Co., Ltd .; Smoyl P-350P; boiling point 480 ° C.) and decalin so that the polyethylene concentration becomes 30% by weight. A polyethylene solution was prepared by dissolving in a mixed solvent. The composition of this polyethylene solution was polyethylene: liquid paraffin: decalin = 30: 45: 25 (weight ratio).
This polyethylene solution was extruded from a die at 148 ° C. and cooled in a water bath to prepare a gel tape (base tape). The base tape was dried at 60 ° C. for 8 minutes and at 95 ° C. for 15 minutes, and then the base tape was stretched by biaxial stretching that was performed in the order of longitudinal stretching and lateral stretching. Here, the longitudinal stretching was 5.5 times, the stretching temperature was 90 ° C., the transverse stretching was 11.0 times the stretching ratio, and the stretching temperature was 105 ° C. After transverse stretching, heat setting was performed at 125 ° C. Next, this was immersed in a methylene chloride bath to extract liquid paraffin and decalin. Then, it dried at 50 degreeC and annealed at 120 degreeC, and obtained PE microporous film.

(ii) Production of polymetaphenylene isophthalamide In a reaction vessel equipped with a thermometer, a stirrer and a raw material inlet, 753 g of NMP having a water content of 100 ppm or less was placed. 5 g was dissolved and cooled to 0 ° C. To this cooled diamine solution, 160.5 g of isophthalic acid chloride was gradually added with stirring to react. This reaction increased the temperature of the solution to 70 ° C. After the change in viscosity stopped, 58.4 g of calcium hydroxide powder was added and stirred for another 40 minutes to complete the reaction, and the polymerization solution was taken out and reprecipitated in water to obtain 184.0 g of polymetaphenylene isophthalamide. .

(iii) Production of activated alumina Aluminum hydroxide (manufactured by Showa Denko; H-43M) was heat-treated at 280 ° C. to obtain activated alumina having an average particle diameter of 0.8 μm and a specific surface area of 400 m ² / g. The true density of this activated alumina was 3.1 g / cm ² . Also, when XRD analysis was performed, a peak derived from boehmite was observed in a broad chart, and the integrated intensity of the peak at 2θ = 14.39 ° was 98 cps · deg. The integrated intensity was 0.07 with respect to the integrated intensity of the broad peak existing over 2θ = 10 to 60 deg. Therefore, this activated alumina can be said to be amorphous alumina because it mainly has an amorphous bulk structure and a very small amount of boehmite phase is mixed.

(iv) Manufacture of laminated separator The polymetaphenylene isophthalamide and activated alumina obtained as described above were prepared so as to have a weight ratio of 40:60, and these had a polymetaphenylene isophthalamide concentration of 5. Dimethylacetamide (DMAc) and tripropylene glycol (TPG) were mixed in a mixed solvent having a weight ratio of 50:50 so as to be 5% by weight to obtain a slurry for coating.
The coating slurry was applied to both sides of the PE film by placing an appropriate amount of the coating slurry on a Meyer bar and passing the PE film obtained as described above between a pair of Meyer bars. This was immersed in a coagulation liquid having a weight ratio of water: DMAc: TPG = 50: 25: 25 and 40 ° C. Thereafter, the obtained film was washed with water and dried. Thereby, the laminated separator with which the heat resistant porous layer was coated was obtained.

(v) Production of positive electrode 89.5 parts by weight of lithium cobaltate (LiCoO ₂ , manufactured by Nippon Chemical Industry Co., Ltd.), 4.5 parts by weight of acetylene black (Denka Black, manufactured by Denki Kagaku Kogyo Co., Ltd.) and polyvinylidene fluoride (Clare) A positive electrode paste was prepared by using 6 wt% of an NMP solution of polyvinylidene fluoride so that the dry weight of Chemical Industries, Ltd. was 6 parts by weight. The obtained paste was applied onto an aluminum foil having a thickness of 20 μm, dried and pressed to obtain a positive electrode having a thickness of 97 μm.

(vi) Production of Negative Electrode As a negative electrode active material, 87 parts by weight of mesophase carbon microbeads (MCMB, manufactured by Osaka Gas Chemical Co., Ltd.), 3 parts by weight of acetylene black and 10 parts by weight of polyvinylidene fluoride were prepared. A negative electrode agent paste was prepared using an NMP solution of 6% by weight of polyvinylidene fluoride. The obtained paste was applied onto a copper foil having a thickness of 18 μm, dried and pressed to prepare a negative electrode having a thickness of 90 μm.

(vii) Preparation of ethylene carbonate and ethyl methyl carbonate in the nonaqueous electrolyte 3: 7 solution were mixed in a weight ratio of, were used as LiPF ₆ was dissolved at a 1 mol / L.

(viii) Production of non-aqueous secondary battery The positive electrode and negative electrode obtained as described above were opposed to each other through a laminated separator. This was impregnated with a non-aqueous electrolyte and sealed in an exterior made of an aluminum laminate film to produce a non-aqueous secondary battery.

[Reference Comparative Example 3-1]
As polyethylene powder, GUR2126 (weight average molecular weight 41.50 million, melting point 141 ° C.) and GRX143 (weight average molecular weight 560,000, melting point 135 ° C.) manufactured by Ticona were used. GUR2126 and GURX143 are made to be 1: 9 (weight ratio), and liquid paraffin (manufactured by Matsumura Oil Research Co., Ltd .; Smoyl P-350P; boiling point 480 ° C.) and decalin so that the polyethylene concentration becomes 30% by weight. It was dissolved in a mixed solvent, and α-alumina (AL-160SG-3; manufactured by Showa Denko) having an average particle size of 0.5 μm and a specific surface area of 7 m ² / g was dispersed as a filler to prepare a polyethylene solution. The composition of this polyethylene solution was polyethylene: alumina: liquid paraffin: decalin = 30: 10: 55: 30 (weight ratio).
This polyethylene solution was extruded from a die at 148 ° C. and cooled in a water bath to prepare a gel tape (base tape). The base tape was dried at 60 ° C. for 8 minutes and at 95 ° C. for 15 minutes, and then the base tape was stretched by biaxial stretching that was performed in the order of longitudinal stretching and lateral stretching. Here, the longitudinal stretching was 5.5 times, the stretching temperature was 90 ° C., the transverse stretching was 11.0 times the stretching ratio, and the stretching temperature was 105 ° C. After transverse stretching, heat setting was performed at 125 ° C. Next, this was immersed in a methylene chloride bath to extract liquid paraffin and decalin. Then, it dried at 50 degreeC and annealed at 120 degreeC, and obtained the separator which consists of PE microporous films.
A nonaqueous secondary battery was produced in the same manner as in Reference Example 3-1, except that this separator was used.

[Reference Comparative Example 3-2]
Aluminum hydroxide (Showa Denko; H-43M) was heat-treated at 220 ° C. to obtain activated alumina having an average particle diameter of 0.8 μm and a specific surface area of 60 m ² / g. The true density of this activated alumina was 2.5 g / cm ² . Further, in XRD, a broad peak derived from the amorphous structure was not confirmed, and a peak derived from gibbsite was clearly observed. Therefore, the bulk structure of this activated alumina was mainly gibbsite.
A nonaqueous secondary battery was obtained in the same manner as in Reference Comparative Example 3-1, except that this activated alumina was used as an inorganic filler.

[Reference Comparative Example 3-3]
Aluminum hydroxide (Showa Denko; H-43M) was heat-treated at 240 ° C. to obtain activated alumina having an average particle diameter of 0.8 μm and a specific surface area of 200 m ² / g. The true density of this activated alumina was 2.6 g / cm ² . Further, when XRD analysis was performed on this activated alumina, a peak derived from gibbsite was observed, the integrated intensity of the peak at 2θ = 18.27 ° was 371 cps · deg, and the integrated intensity of this main peak was 2θ = It was 0.35 with respect to the integrated intensity | strength of the broad peak which exists over 10-60deg. Therefore, the bulk structure of this activated alumina was mainly gibbsite.
A nonaqueous secondary battery was obtained in the same manner as in Reference Comparative Example 3-1, except that this activated alumina was used as an inorganic filler.

[Reference Comparative Example 3-4]
A non-aqueous secondary battery was obtained in the same manner as Reference Comparative Example 3-1, except that zeolite (HSZ-980HOA; manufactured by Tosoh Corporation) having an average particle diameter of 2 μm and a specific surface area of 400 m ² / g was used as the inorganic filler. .

[Reference Comparative Example 3-5]
A non-aqueous secondary battery was prepared in the same manner as Reference Comparative Example 3-1, except that silica having an average particle diameter of 2 μm and a specific surface area of 300 m ² / g was used as the inorganic filler (Tokai Chemical Industries, Ltd .; ML-384). Obtained.

[Reference Comparative Example 3-6]
Activated carbon (manufactured by Kansai Thermal Chemical Co., Ltd .; MSP-20) is subjected to wet pulverization (2 mm zirconia bead mill) using dimethylacetamide (DMAc) as a dispersion solvent, whereby an average particle diameter of 0.6 μm and a specific surface area of 1600 m ² / g of activated carbon was obtained.
A nonaqueous secondary battery was obtained in the same manner as in Reference Comparative Example 3-1, except that this activated carbon was used as an inorganic filler.

[Measurement of capacity maintenance ratio]
About the non-aqueous secondary battery of the Example produced as mentioned above and a comparative example, in a 60 degreeC thermostat, a charge / discharge measuring apparatus (HJ-101SM6 by Hokuto Denko Co., Ltd.) was used, and charge / discharge characteristics were measured. did. Regarding charging / discharging conditions, charging is performed at 0.2 C to 4.2 V for 8 hours, discharging is performed at 0.2 C at 2.75 V, and the capacity maintenance rate is the discharge at the time of 500 cycles with respect to the initial discharging capacity. The capacity ratio. Table 7 shows the measurement results.

As can be seen from Table 7, Reference Example 3-1 using activated alumina having a specific surface area of 300 to 1000 m ² / g is activated alumina having a specific surface area outside the above range (Reference Comparative Examples 3-2 and 3-3). ), Α-alumina (Reference Comparative Example 3-1), and other porous fillers (Reference Comparative Examples 3-3 to 3-6), the capacity retention rate after 500 cycle characteristic tests is remarkably excellent. ing. This is presumably because the activated alumina having a specific surface area of 300 to 1000 m ² / g reduced the activity of HF in the battery. In the reference example, the filler is applied in the heat-resistant porous layer in the composite separator, and in the reference comparative example, there is a difference that the filler is applied in the PE separator, but both apply the filler in the separator. The above-mentioned difference is not so large that the above-mentioned difference has an influence on the capacity retention rate.

(4) About the effect of the amorphous alumina in a 4th form Hereinafter, the structure using an amorphous alumina is examined among the 4th forms of this invention. Various measurement methods are as described above.

[Reference Example 4-1]
A nonaqueous secondary battery of Reference Example 4-1 was produced in the same manner as Reference Example 3-1.

[Reference Comparative Example 4-1]
As polyethylene powder, GUR2126 (weight average molecular weight 41.50 million, melting point 141 ° C.) and GRX143 (weight average molecular weight 560,000, melting point 135 ° C.) manufactured by Ticona were used. GUR2126 and GURX143 are made to be 1: 9 (weight ratio), and liquid paraffin (manufactured by Matsumura Oil Research Co., Ltd .; Smoyl P-350P; boiling point 480 ° C.) and decalin so that the polyethylene concentration becomes 30% by weight. It was dissolved in a mixed solvent, and α-alumina (AL-160SG-3; manufactured by Showa Denko) having an average particle size of 0.5 μm and a specific surface area of 7 m ² / g was dispersed as a filler to prepare a polyethylene solution. The composition of this polyethylene solution was polyethylene: alumina: liquid paraffin: decalin = 30: 10: 55: 30 (weight ratio).
This polyethylene solution was extruded from a die at 148 ° C. and cooled in a water bath to prepare a gel tape (base tape). The base tape was dried at 60 ° C. for 8 minutes and at 95 ° C. for 15 minutes, and then the base tape was stretched by biaxial stretching that was performed in the order of longitudinal stretching and lateral stretching. Here, the longitudinal stretching was 5.5 times, the stretching temperature was 90 ° C., the transverse stretching was 11.0 times the stretching ratio, and the stretching temperature was 105 ° C. After transverse stretching, heat setting was performed at 125 ° C. Next, this was immersed in a methylene chloride bath to extract liquid paraffin and decalin. Then, it dried at 50 degreeC and annealed at 120 degreeC, and obtained the separator which consists of PE microporous films.
A non-aqueous secondary battery was produced in the same manner as in Reference Example 3-1, except that this separator was used.

[Reference Comparative Example 4-2]
A non-aqueous two-material system was prepared in the same manner as in Reference Comparative Example 4-1, except that non-porous alumina (manufactured by Daimei Chemical Industries; C06) having an average particle diameter of 0.6 μm and a specific surface area of 15 m ² / g was used as the inorganic filler. The next battery was obtained. When this alumina was subjected to XRD analysis, a clear peak derived from boehmite was observed.

[Reference Comparative Example 4-3]
Except for using non-porous aluminum hydroxide (manufactured by Showa Denko; H-43M) having an average particle diameter of 0.8 μm and a specific surface area of 7 m ² / g as the inorganic filler, A non-aqueous secondary battery was obtained. When this aluminum hydroxide was subjected to XRD analysis, a clear peak derived from gibbsite was observed.

[Measurement of capacity maintenance ratio]
About the non-aqueous secondary battery of the Example produced as mentioned above and a comparative example, in a 60 degreeC thermostat, a charge / discharge measuring apparatus (HJ-101SM6 by Hokuto Denko Co., Ltd.) was used, and charge / discharge characteristics were measured. did. Regarding charging / discharging conditions, charging is performed at 0.2 C to 4.2 V for 8 hours, discharging is performed at 0.2 C at 2.75 V, and the capacity retention rate is discharging at 400 cycles with respect to the initial discharging capacity. The capacity ratio. Table 8 shows the measurement results.

  As can be seen from Table 8, Reference Example 4-1 using amorphous alumina is α-alumina (Reference Comparative Example 4-1), boehmite (Reference Comparative Example 4-2), Gibbsite (Reference Comparative Example 4-3). Compared to other alumina fillers, etc., the capacity retention rate after 400 cycle characteristic tests is remarkably superior. This is presumably because amorphous alumina lowered the activity of HF in the battery.

(5) Examples according to the fifth mode Hereinafter, examples according to the fifth mode of the present invention will be described. The average particle diameter, specific surface area, true density, crystal structure and element ratio, and film thickness measuring method of the inorganic filler are as described above.

[Example 1-1]
(i) Production of activated alumina Activated alumina A was produced in the same manner as in Reference Example 3-1.
(ii) Production of positive electrode, negative electrode, and nonaqueous electrolyte The positive electrode, the negative electrode, and the nonaqueous electrolyte were also produced in the same manner as in Reference Example 3-1.
(iii) Manufacture of separator As polyethylene powder, GUR2126 (weight average molecular weight 41.50 million, melting point 141.degree. C.) and GURX 143 (weight average molecular weight 560,000, melting point 135.degree. C.) manufactured by Ticona were used. GUR2126 and GURX143 are made to be 1: 9 (weight ratio), and liquid paraffin (manufactured by Matsumura Oil Research Co., Ltd .; Smoyl P-350P; boiling point 480 ° C.) and decalin so that the polyethylene concentration becomes 30% by weight. It was dissolved in a mixed solvent, and the activated alumina A was dispersed as an inorganic filler to prepare a polyethylene solution. The composition of this polyethylene solution was polyethylene: inorganic filler: liquid paraffin: decalin = 30: 10: 55: 30 (weight ratio).
This polyethylene solution was extruded from a die at 148 ° C. and cooled in a water bath to prepare a gel tape (base tape). The base tape was dried at 60 ° C. for 8 minutes and at 95 ° C. for 15 minutes, and then the base tape was stretched by biaxial stretching that was performed in the order of longitudinal stretching and lateral stretching. Here, the longitudinal stretching was 5.5 times, the stretching temperature was 90 ° C., the transverse stretching was 11.0 times the stretching ratio, and the stretching temperature was 105 ° C. After transverse stretching, heat setting was performed at 125 ° C. Next, this was immersed in a methylene chloride bath to extract liquid paraffin and decalin. Then, it dried at 50 degreeC and annealed at 120 degreeC, and obtained the PE separator which consists of a polyethylene microporous film.
(iv) Non-aqueous secondary battery The positive electrode and the negative electrode obtained as described above were opposed to each other with a separator interposed therebetween. This was impregnated with a non-aqueous electrolyte and sealed in an exterior made of an aluminum laminate film to produce a non-aqueous secondary battery according to an example of the present invention.

[Example 1-2]
Aluminum hydroxide (Showa Denko; H-43M) was heat treated at 260 ° C. to obtain activated alumina B having an average particle diameter of 0.8 μm, a specific surface area of 350 m ² / g, and a true density of 3.0 g / cm ³ . A structural analysis of this activated alumina B by XRD revealed that a peak derived from boehmite was slightly observed in a broad chart, and the integrated intensity of the peak at 2θ = 14.40 ° was 83 cps · deg. The integrated intensity of the peak was 0.05 with respect to the integrated intensity of the broad peak existing over 2θ = 10 to 60 deg. Therefore, this activated alumina mainly has an amorphous bulk structure and a very small amount of boehmite phase was mixed.
A nonaqueous secondary battery of the present invention was obtained in the same manner as Example 1-1 except that this activated alumina B was used as an inorganic filler.

[Example 1-3]
Polymer (weight average molecular weight 400000) copolymerized in a molar ratio of vinylidene fluoride: hexafluoropropylene: chlorotrifluoroethylene = 97: 1: 2, the above-mentioned activated alumina A, dimethylacetamide (DMAc), and tri The dope was obtained by sufficiently stirring so that the weight ratio of propylene glycol (TPG) was polymer: active alumina: DMAc: TPG = 12: 4: 49: 35. Then, a nonwoven fabric composed of PET short fibers and polyolefin short fibers was sufficiently impregnated with the dope, solidified in a coagulation bath, washed and dried. This obtained the composite separator (PVdF / nonwoven fabric separator) of polyvinylidene fluoride and the nonwoven fabric. The composition of the coagulation bath was water: dimethylacetamide: tripropylene glycol = 57: 30: 13 by weight ratio. And the non-aqueous secondary battery of this invention was obtained like Example 1-1 except having used PVdF / nonwoven fabric separator instead of PE separator.

[Example 1-4]
A coating solution was prepared by mixing 5 parts by weight of polyvinylidene fluoride, 1 part by weight of activated alumina A, and 94 parts by weight of DMAc and stirring sufficiently to obtain a uniform solution. And after apply | coating said coating liquid to the single side | surface of a polypropylene separator (Celgard # 2400) with the bar coater, this was dried at 60 degreeC. As a result, a polypropylene separator (PVdF / PP separator) having a coating layer having a thickness of 4 μm was obtained. And the nonaqueous secondary battery of this invention was obtained like Example 1-1 except having used the PVdF / PP separator so that the coating layer might contact | connect a positive electrode instead of PE separator.

[Example 1-5]
A nonaqueous secondary battery of the present invention was obtained in the same manner as in Example 1-4, except that the PVdF / PP separator obtained in Example 1-4 was used so that the coating layer was in contact with the negative electrode.

[Example 1-6]
89.5 parts by weight of lithium manganate (LiMn ₂ O ₄ , manufactured by JGC Chemical Co., Ltd.), 4.5 parts by weight of acetylene black (Denka Black, manufactured by Denki Kagaku Kogyo Co., Ltd.) and polyvinylidene fluoride (manufactured by CLEA Chemical Industries, Ltd.) A positive electrode paste was prepared using 6 wt% of an NMP solution of polyvinylidene fluoride so that the dry weight of 6) was 6 parts by weight. The obtained paste was applied onto an aluminum foil having a thickness of 20 μm, dried and pressed to obtain a positive electrode having a thickness of 70 μm.
A nonaqueous secondary battery of the present invention was obtained in the same manner as Example 1-1 except that this positive electrode was used.

[Example 1-7]
89.5 parts by weight of lithium cobaltate (LiCoO ₂ , manufactured by Nippon Chemical Industry Co., Ltd.) powder, 4.5 parts by weight of acetylene black (Denka Black, manufactured by Denki Kagaku Kogyo Co., Ltd.), 3 parts by weight of activated alumina A and polyvinylidene fluoride ( A positive electrode agent paste was prepared by using 6 wt% of an NMP solution of polyvinylidene fluoride so that the dry weight of Claire Chemical Industries, Ltd. was 6 parts by weight. The obtained paste was applied onto an aluminum foil having a thickness of 20 μm, dried and pressed to obtain a positive electrode having a thickness of 97 μm.
As polyethylene powder, GUR2126 (weight average molecular weight 41.50 million, melting point 141 ° C.) and GRX143 (weight average molecular weight 560,000, melting point 135 ° C.) manufactured by Ticona were used. GUR2126 and GURX143 are made to be 1: 9 (weight ratio), and liquid paraffin (manufactured by Matsumura Oil Research Co., Ltd .; Smoyl P-350P; boiling point 480 ° C.) and decalin so that the polyethylene concentration becomes 30% by weight. A polyethylene solution was prepared by dissolving in a mixed solvent. The composition of this polyethylene solution was polyethylene: liquid paraffin: decalin = 30: 45: 25 (weight ratio).
This polyethylene solution was extruded from a die at 148 ° C. and cooled in a water bath to prepare a gel tape (base tape). The base tape was dried at 60 ° C. for 8 minutes and at 95 ° C. for 15 minutes, and then the base tape was stretched by biaxial stretching that was performed in the order of longitudinal stretching and lateral stretching. Here, the longitudinal stretching was 5.5 times, the stretching temperature was 90 ° C., the transverse stretching was 11.0 times the stretching ratio, and the stretching temperature was 105 ° C. After transverse stretching, heat setting was performed at 125 ° C. Next, this was immersed in a methylene chloride bath to extract liquid paraffin and decalin. Then, it dried at 50 degreeC and annealed at 120 degreeC, and obtained the PE separator which consists of a polyethylene microporous film.
A nonaqueous secondary battery of the present invention was obtained in the same manner as in Example 1-1 except that the positive electrode and PE separator produced as described above were used.

[Example 1-8]
As negative electrode active material, 87 parts by weight of mesophase carbon microbeads (MCMB, manufactured by Osaka Gas Chemical Co., Ltd.), 3 parts by weight of acetylene black, 3 parts by weight of activated alumina A, and 10 parts by weight of dry weight of polyvinylidene fluoride As described above, a negative electrode agent paste was prepared using an NMP solution of 6% by weight of polyvinylidene fluoride. The obtained paste was applied onto a copper foil having a thickness of 18 μm, dried and pressed to produce a negative electrode having a thickness of 91 μm.
A nonaqueous secondary battery of the present invention was obtained in the same manner as in Example 1-1 except that this negative electrode was used and the PE separator in Example 1-7 was used.

[Example 1-9]
The coating liquid prepared in Example 1-4 was applied to the active material side of the positive electrode manufactured in Example 1-1 using a bar coater, and then dried at 60 ° C. As a result, a positive electrode having a coating layer (positive electrode surface layer) having a thickness of 4 μm was obtained.
A nonaqueous secondary battery of the present invention was obtained in the same manner as in Example 1-1, except that this positive electrode was used and the PE separator in Example 1-7 was used.

[Example 1-10]
The coating liquid prepared in Example 1-4 was applied to the active material side of the negative electrode manufactured in Example 1-1 using a bar coater, and then dried at 60 ° C. As a result, a negative electrode having a coating layer (negative electrode surface layer) having a thickness of 4 μm was obtained.
A nonaqueous secondary battery of the present invention was obtained in the same manner as in Example 1-1 except that this negative electrode was used and the PE separator in Example 1-7 was used.

[Comparative Example 1-1]
A non-aqueous secondary battery was obtained in the same manner as in Example 1-1 except that the PE separator in Example 1-7 was used.

[Comparative Example 1-2]
Weight of copolymer (weight average molecular weight 400000), dimethylacetamide (DMAc), and tripropylene glycol (TPG) copolymerized at a molar ratio of vinylidene fluoride: hexafluoropropylene: chlorotrifluoroethylene = 97: 1: 2. The dope was obtained by sufficiently stirring so that the ratio was polymer: DMAc: TPG = 12: 48: 40. Then, a nonwoven fabric composed of PET short fibers and polyolefin short fibers was sufficiently impregnated with the above dope, solidified in a coagulation bath, washed with water and dried. Thereby, a separator (PVdF / nonwoven fabric separator) in which polyvinylidene fluoride was combined with a nonwoven fabric was obtained. The composition of the coagulation bath was water: dimethylacetamide: tripropylene glycol = 57: 30: 13 by weight ratio.
A non-aqueous secondary battery was obtained in the same manner as in Example 1-1 except that this PVdF / nonwoven fabric separator was used.

[Comparative Example 1-3]
A non-aqueous secondary battery was obtained in the same manner as in Comparative Example 1 except that a polypropylene separator (Celguard # 2400) was used instead of the PE separator.

[Comparative Example 1-4]
A non-aqueous two-particle system was prepared in the same manner as in Example 1-1 except that α-alumina (AL-160SG-3; manufactured by Showa Denko) having an average particle size of 0.5 μm and a specific surface area of 7 m ² / g was used as the inorganic filler. The next battery was obtained.

[Comparative Example 1-5]
Aluminum hydroxide (Showa Denko; H-43M) was heat-treated at 220 ° C. to obtain activated alumina C having an average particle diameter of 0.8 μm, a specific surface area of 60 m ² / g, and a true density of 2.5 g / cm ³ . When the crystal structure of this activated alumina C was analyzed by XRD, the broad peak derived from the amorphous structure was not confirmed, and the peak derived from the gibbsite was clearly observed. I found out.
A nonaqueous secondary battery was obtained in the same manner as in Example 1-1 except that this activated alumina C was used as an inorganic filler.

[Comparative Example 1-6]
Aluminum hydroxide (Showa Denko; H-43M) was heat-treated at 240 ° C. to obtain activated alumina D having an average particle diameter of 0.8 μm, a specific surface area of 200 m ² / g, and a true density of 2.6 g / cm ³ . When the crystal structure of this activated alumina D was analyzed by XRD, a peak derived from gibbsite was observed, the integrated intensity of the peak at 2θ = 18.27 ° was 371 cps · deg, and the integrated intensity of this main peak was 2θ. It was 0.35 with respect to the integrated intensity of the broad peak which exists over 10-60deg. Therefore, it turned out that activated alumina D contains gibbsite in the bulk structure.
A nonaqueous secondary battery was obtained in the same manner as in Example 1-1 except that this activated alumina D was used as an inorganic filler.

[Comparative Example 1-7]
A nonaqueous secondary battery was obtained in the same manner as in Example 1-1 except that zeolite (HSZ-980HOA; manufactured by Tosoh Corporation) having an average particle diameter of 2 μm and a specific surface area of 400 m ² / g was used as the inorganic filler.

[Comparative Example 1-8]
In the same manner as in Example 1 except that silica having an average particle diameter of 2 μm and a specific surface area of 300 m ² / g was used as the inorganic filler, and non-activated alumina was used, ML-384 was used. An aqueous secondary battery was obtained.

[Comparative Example 1-9]
Activated carbon (manufactured by Kansai Thermal Chemical Co., Ltd .; MSP-20) is subjected to wet pulverization (2 mm zirconia bead mill) using dimethylacetamide (DMAc) as a dispersion solvent, whereby an average particle diameter of 0.6 μm and a specific surface area of 1600 m ² / g of activated carbon was obtained.
A nonaqueous secondary battery was obtained in the same manner as Example 1-1 except that this activated carbon was used as an inorganic filler.

[Comparative Example 1-10]
A non-aqueous secondary battery was obtained in the same manner as in Comparative Example 1-1 except that the positive electrode produced in Example 1-6 was used.

[Measurement of capacity maintenance ratio]
About the non-aqueous secondary battery of the Example produced as mentioned above and a comparative example, in a 60 degreeC thermostat, a charge / discharge measuring apparatus (HJ-101SM6 by Hokuto Denko Co., Ltd.) was used, and charge / discharge characteristics were measured. did. Regarding charging / discharging conditions, charging is performed at 0.2 C to 4.2 V for 8 hours, discharging is performed at 0.2 C at 2.75 V, and the capacity maintenance rate is the discharge at the time of 500 cycles with respect to the initial discharging capacity. The capacity ratio. Table 9 shows the measurement results.

[Performance evaluation]
As can be seen from the results of Examples 1-1 to 1-3 and Comparative Examples 1-1 to 1-3, all of the examples containing activated alumina in the separator showed excellent capacity retention of 70% or more. However, Comparative Examples 1-1 to 1-3 not containing activated alumina had a capacity retention rate as low as about 50%. Furthermore, although Examples 1-3 to 1-5 have a configuration in which a layer containing activated alumina is laminated on the separator, the capacity retention rate was excellent at 70% in all cases. Further, comparison between Examples 1-4 and 1-5 also confirmed that it was effective if a layer containing active alumina was present in at least one of the positive electrode and the negative electrode.

As can be seen from the results of Examples 1-1 to 1-2 and Comparative Examples 1-4 to 1-6, a tendency that the capacity retention rate was excellent as the specific surface area of the activated alumina increased was observed. And since the effect was inadequate in the specific surface area 200m < ² > / g of the comparative example 1-6 and the specific surface area of Example 1-2 was 350 m < ² > / g, the effect could fully be confirmed. It can be said that the specific surface area of the activated alumina is preferably 300 m ² / g or more. In Comparative Examples 1-7 and 1-8, zeolite and silica having a specific surface area of 300 m ² / g or more were used instead of activated alumina. Did not show. In addition, Comparative Example 1-9 using activated carbon having a specific surface area of 1600 m ² / g had a capacity retention rate as low as 62% compared to Examples 1-1 to 1-2. From this, it can be said that the specific surface area is preferably 1000 m ² / g or less, more preferably 500 m ² / g or less. On the other hand, the true density in the 2.7 g / cm ³ or less and 3.9 g / cm ³ but with low capacity retention rate, the obtained better results if the range of 2.8~3.3g / cm ³ I understood. Based on the above, it can be estimated that the capacity maintenance rate has improved because the surface condition peculiar to activated alumina has reduced the activity of HF.

Even in Examples 1-6 and Comparative Example 1-10 in which the positive electrode active material was lithium manganate, excellent results were obtained with a capacity retention rate of 70% or more by using a separator containing activated alumina. In Comparative Example 1-10, since lithium manganate was used, the metal from the positive electrode was dissolved by HF than lithium cobaltate, so the capacity retention rate was considered to be as low as 42%.
Comparing the system containing activated alumina in the electrode with Examples 1-7 to 1-10, which is a system in which an activated alumina layer is laminated on the electrode surface, the capacity retention rate is 70% or more in all Examples. Are better. As a result, it was confirmed that the location of the activated alumina was effective even if contained in the electrode or laminated on the electrode surface.
Summarizing the above performance evaluation results, in order to obtain a non-aqueous secondary battery with an excellent capacity retention rate, it is necessary to contain activated alumina having a specific surface area of 300 to 1000 m ² / g in the non-aqueous secondary battery. It was found as a finding that the location of the activated alumina is not particularly limited.

[HF removal performance]
For the non-aqueous secondary batteries of Examples 1-1 and 1-2 and Comparative Example 1-1 described above, the capacity retention rate was measured, and then the batteries were disassembled to extract a non-aqueous electrolyte. And content of HF in this electrolyte was measured.
Specifically, the HF content is measured by disassembling the non-aqueous secondary battery after measuring the capacity retention rate, and then in a predetermined amount of solution in which ethylene carbonate and ethyl methyl carbonate are mixed at a weight ratio of 3: 7. And left for 1 week to extract HF present in the battery with a solution. Then, titration was performed with an aqueous sodium hydroxide solution using bromothymol blue as an indicator, and the acid concentration in the extracted solution was determined. Finally, the value obtained by converting the obtained acid concentration per weight of the electrolyte used in the non-aqueous secondary battery was defined as the HF content (ppm). The measurement results for each sample are shown in Table 10 below. The HF content in the electrolyte before constituting the battery was 30 ppm.

  As can be seen from the results in Table 10, it can be seen that in the batteries using the activated aluminas of Examples 1-1 and 1-2, the residual amount of HF is small as compared with Comparative Example 1-1. This is considered to be because HF is suitably captured by the activated alumina in the present invention.

(6) Example according to Sixth Mode Hereinafter, an example according to the sixth mode of the present invention will be described. The average particle diameter, specific surface area, true density, crystal structure and element ratio, and film thickness measuring method of the inorganic filler are as described above.
[Example 2-1]
A non-aqueous secondary battery was produced in the same manner as Example 1-1 described above.
[Example 2-2]
A non-aqueous secondary battery was produced in the same manner as Example 1-2 described above.
[Example 2-3]
A non-aqueous secondary battery was produced in the same manner as in Example 1-3 described above.
[Example 2-4]
A non-aqueous secondary battery was produced in the same manner as in Example 1-4 described above.
[Example 2-5]
A non-aqueous secondary battery was produced in the same manner as Example 1-5 described above.
[Example 2-6]
A non-aqueous secondary battery was produced in the same manner as Example 1-9 described above.
[Example 2-7]
A non-aqueous secondary battery was produced in the same manner as Example 1-10 described above.

[Comparative Example 2-1]
A non-aqueous secondary battery was produced in the same manner as Comparative Example 1-1 described above.
[Comparative Example 2-2]
A non-aqueous secondary battery was produced in the same manner as Comparative Example 1-2 described above.
[Comparative Example 2-3]
A non-aqueous secondary battery was produced in the same manner as Comparative Example 1-3 described above.
[Comparative Example 2-4]
Example in which non-porous alumina E (manufactured by Showa Denko; AL-160SG-3) having an average particle diameter of 0.5 μm and a specific surface area of 7 m ² / g was used without using alumina A as an inorganic filler. A non-aqueous secondary battery was obtained in the same manner as in 2-1. When this alumina E was subjected to XRD analysis, a clear peak derived from α-alumina was observed.
[Comparative Example 2-5]
Example 2-1 except that alumina A was not used as the inorganic filler, and nonporous alumina F (Daimei Chemical; C06) having an average particle diameter of 0.6 μm and a specific surface area of 15 m ² / g was used. In the same manner as above, a non-aqueous secondary battery was obtained. When this alumina F was subjected to XRD analysis, a clear peak derived from boehmite was observed.
[Comparative Example 2-6]
Example 2 except that alumina A was not used as a filler, and nonporous aluminum hydroxide (manufactured by Showa Denko; H-43M) having an average particle diameter of 0.8 μm and a specific surface area of 7 m ² / g was used. In the same manner as in Example 1, a non-aqueous secondary battery was obtained. When this aluminum hydroxide was subjected to XRD analysis, a clear peak derived from gibbsite was observed.
[Comparative Example 2-7]
A non-aqueous secondary battery was produced in the same manner as Comparative Example 1-7 described above.
[Comparative Example 2-8]
Except that alumina (A) was not used as an inorganic filler and silica having an average particle diameter of 2 μm and a specific surface area of 600 m ² / g (made by Tokai Chemical Industries, Ltd .; ML-644) was used, the same as in Example 2-1. Thus, a non-aqueous secondary battery was obtained.
[Comparative Example 2-9]
A non-aqueous secondary battery was produced in the same manner as Comparative Example 1-9 described above.

[Measurement of capacity maintenance ratio]
About the non-aqueous secondary battery of the Example produced as mentioned above and a comparative example, in a 60 degreeC thermostat, a charge / discharge measuring apparatus (HJ-101SM6 by Hokuto Denko Co., Ltd.) was used, and charge / discharge characteristics were measured. did. Regarding charging / discharging conditions, charging is performed at 0.2 C to 4.2 V for 8 hours, discharging is performed at 0.2 C at 2.75 V, and the capacity retention rate is discharging at 400 cycles with respect to the initial discharging capacity. The capacity ratio. Table 11 shows the measurement results.

[140 ° C oven test]
The non-aqueous secondary batteries of Examples and Comparative Examples produced as described above were charged at 0.2 C to 4.2 V for 8 hours, and then stored in an anti-drying dryer at 140 ° C. for 24 hours. As a result, when ignition was confirmed, it evaluated as x, and when ignition was not confirmed, it evaluated as (circle). The results are shown in Table 11.

[Performance evaluation]
In Table 11, from the results of Examples 2-1 to 2-2 and Comparative Examples 2-1 to 2-6, if the structure contains amorphous alumina in the separator, an excellent capacity retention rate of 70% or more It can be seen that Comparative Examples 2-1 to 6-3 not containing a filler had a capacity retention rate as low as 60% or less. Furthermore, from 140 degreeC oven test, although ignition was not confirmed in Examples 2-1 to 2-2, since ignition was confirmed in Comparative Example 2-1, Examples 2-1 to 2-2 were internal. It was found that the safety in short circuit is also excellent.
Further, in the comparison of the structures of alumina, Comparative Examples 2-4 to 2-6 having a structure other than amorphous had a capacity retention rate as low as 60% or less, and further ignition was confirmed in a 140 ° C. oven test. This indicates that amorphous alumina is excellent in both cycle characteristics and safety in internal short circuit.
Moreover, although zeolite, silica, and activated carbon were evaluated in Comparative Examples 2-7 to 2-9 as other inorganic fillers, the capacity retention rate was slightly over 60% compared to Examples 2-1 to 2-2. Low, ignition was confirmed in the 140 ° C. oven test. This also shows that amorphous alumina is excellent as the inorganic filler to be added.
When Examples 2-1 to 2-8 were compared as the location where alumina was present, the capacity retention rate was excellent at 70% or more in all cases, and the presence of amorphous alumina was positive because it did not ignite in the oven test. It was found that if it exists in any part between the negative electrode and the negative electrode, the cycle characteristics and safety due to internal short circuit are excellent.

[Measurement of heat shrinkage]
In order to investigate the cause of the presence or absence of ignition in a 140 ° C. oven test, the thermal contraction rate was measured for the separators of Examples 2-1 to 2-2 and Comparative Examples 2-1 and 2-4 to 2-9. .
Specifically, first, a separator as a sample was cut in a direction of 18 cm (MD direction) × 6 cm (TD). On the line that bisects the TD direction, points (point A, point B) of 2 cm and 17 cm from the top were marked. In addition, marks were placed at 1 cm and 5 cm from the left on the line that bisects the MD direction. This was clipped and hung in an oven adjusted to 105 ° C. and heat-treated for 30 minutes under no tension. The length between two points AB and the length between CDs were measured before and after the heat treatment, and the thermal shrinkage rate was obtained from the following two formulas. Table 12 summarizes the measurement results for each sample.
MD direction thermal shrinkage = (length between AB before heat treatment−length between AB after heat treatment) / (length between AB before heat treatment) × 100
TD direction thermal shrinkage = (length between CDs before heat treatment−length between CDs after heat treatment) / (length between CDs before heat treatment) × 100

  From Table 12, Examples 2-1 to 2-2, which did not ignite in the 140 ° C. oven test, had a heat shrinkage ratio of 15% or less in the MD direction and 2% in the TD direction. On the other hand, Comparative Example 2-1 containing no filler, Comparative Examples 2-4 to 2-6 that are alumina or aluminum hydroxide other than amorphous, and Comparative Examples 2-7 to 2 that are fillers other than alumina In 2-9, the thermal shrinkage rate in the MD direction was 20% or more, and the thermal shrinkage rate in the TD direction was 3% or more, which was higher than those in Examples 2-1 to 2-2. From this, when the thermal shrinkage rate is 20% or more in the MD direction and 3% or more in the TD direction, the separator in the non-aqueous secondary battery breaks in the 140 ° C. oven test and causes ignition due to an internal short circuit. I can guess.

  To summarize the above performance evaluation results, in order to obtain a non-aqueous secondary battery with excellent capacity maintenance rate and excellent safety that does not ignite in a 140 ° C. oven test, amorphous alumina is contained between the negative electrode and the positive electrode. The knowledge that it was good to be able to be made was able to be acquired.

Claims (6)

An adsorbent of hydrogen fluoride mixed in a non-aqueous secondary battery,
The adsorbent has a specific surface area of 300 to 1000 m ² / g and is an amorphous activated alumina particle. The adsorbent for a non-aqueous secondary battery according to claim 1, wherein the true density of the activated alumina particles is 2.7 to 3.8 g / cm ³ .   The element ratio of O / Al present on the surface of the activated alumina particles is 1.0 to 2.5 when measured using an X-ray photoelectron spectrometer. The adsorbent for non-aqueous secondary batteries as described. A porous membrane for a non-aqueous secondary battery comprising an inorganic filler and a binder resin,
A porous membrane for a non-aqueous secondary battery comprising the non-aqueous secondary battery adsorbent according to any one of claims 1 to 3 as the inorganic filler. A separator for a non-aqueous secondary battery comprising a porous substrate and a porous layer containing an inorganic filler and a binder resin laminated on one or both surfaces of the porous substrate,
A non-aqueous secondary battery separator comprising the non-aqueous secondary battery adsorbent according to claim 1 as the inorganic filler. A non-aqueous secondary battery comprising a positive electrode, a negative electrode, a non-aqueous electrolyte and a separator,
A non-aqueous secondary battery comprising the non-aqueous secondary battery adsorbent according to any one of claims 1 to 3 in the battery.