WO2022176773A1 - 繊維強化複合材料用エポキシ樹脂組成物、繊維強化複合材料、および繊維強化複合材料の製造方法 - Google Patents
繊維強化複合材料用エポキシ樹脂組成物、繊維強化複合材料、および繊維強化複合材料の製造方法 Download PDFInfo
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- WO2022176773A1 WO2022176773A1 PCT/JP2022/005373 JP2022005373W WO2022176773A1 WO 2022176773 A1 WO2022176773 A1 WO 2022176773A1 JP 2022005373 W JP2022005373 W JP 2022005373W WO 2022176773 A1 WO2022176773 A1 WO 2022176773A1
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- fiber
- epoxy resin
- reinforced composite
- resin composition
- composite material
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- 239000004843 novolac epoxy resin Substances 0.000 description 1
- 239000005011 phenolic resin Substances 0.000 description 1
- 239000000049 pigment Substances 0.000 description 1
- 239000004014 plasticizer Substances 0.000 description 1
- 229920003192 poly(bis maleimide) Polymers 0.000 description 1
- 229920001485 poly(butyl acrylate) polymer Polymers 0.000 description 1
- 229920002857 polybutadiene Polymers 0.000 description 1
- 238000006116 polymerization reaction Methods 0.000 description 1
- 230000000379 polymerizing effect Effects 0.000 description 1
- 229920002223 polystyrene Polymers 0.000 description 1
- 229910052700 potassium Inorganic materials 0.000 description 1
- 239000011591 potassium Substances 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 230000004044 response Effects 0.000 description 1
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 description 1
- 229910010271 silicon carbide Inorganic materials 0.000 description 1
- 229920002050 silicone resin Polymers 0.000 description 1
- 239000011780 sodium chloride Substances 0.000 description 1
- 125000006850 spacer group Chemical group 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 239000004094 surface-active agent Substances 0.000 description 1
- 238000010557 suspension polymerization reaction Methods 0.000 description 1
- YLQBMQCUIZJEEH-UHFFFAOYSA-N tetrahydrofuran Natural products C=1C=COC=1 YLQBMQCUIZJEEH-UHFFFAOYSA-N 0.000 description 1
- 230000008646 thermal stress Effects 0.000 description 1
- 238000002411 thermogravimetry Methods 0.000 description 1
- 230000008719 thickening Effects 0.000 description 1
- 239000006097 ultraviolet radiation absorber Substances 0.000 description 1
- 229920006337 unsaturated polyester resin Polymers 0.000 description 1
- 229920001567 vinyl ester resin Polymers 0.000 description 1
- 239000002759 woven fabric Substances 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08K—Use of inorganic or non-macromolecular organic substances as compounding ingredients
- C08K5/00—Use of organic ingredients
- C08K5/16—Nitrogen-containing compounds
- C08K5/17—Amines; Quaternary ammonium compounds
- C08K5/18—Amines; Quaternary ammonium compounds with aromatically bound amino groups
-
- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08G—MACROMOLECULAR COMPOUNDS OBTAINED OTHERWISE THAN BY REACTIONS ONLY INVOLVING UNSATURATED CARBON-TO-CARBON BONDS
- C08G59/00—Polycondensates containing more than one epoxy group per molecule; Macromolecules obtained by polymerising compounds containing more than one epoxy group per molecule using curing agents or catalysts which react with the epoxy groups
- C08G59/18—Macromolecules obtained by polymerising compounds containing more than one epoxy group per molecule using curing agents or catalysts which react with the epoxy groups ; e.g. general methods of curing
- C08G59/20—Macromolecules obtained by polymerising compounds containing more than one epoxy group per molecule using curing agents or catalysts which react with the epoxy groups ; e.g. general methods of curing characterised by the epoxy compounds used
- C08G59/32—Epoxy compounds containing three or more epoxy groups
- C08G59/3227—Compounds containing acyclic nitrogen atoms
-
- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08G—MACROMOLECULAR COMPOUNDS OBTAINED OTHERWISE THAN BY REACTIONS ONLY INVOLVING UNSATURATED CARBON-TO-CARBON BONDS
- C08G59/00—Polycondensates containing more than one epoxy group per molecule; Macromolecules obtained by polymerising compounds containing more than one epoxy group per molecule using curing agents or catalysts which react with the epoxy groups
- C08G59/18—Macromolecules obtained by polymerising compounds containing more than one epoxy group per molecule using curing agents or catalysts which react with the epoxy groups ; e.g. general methods of curing
- C08G59/20—Macromolecules obtained by polymerising compounds containing more than one epoxy group per molecule using curing agents or catalysts which react with the epoxy groups ; e.g. general methods of curing characterised by the epoxy compounds used
- C08G59/32—Epoxy compounds containing three or more epoxy groups
- C08G59/38—Epoxy compounds containing three or more epoxy groups together with di-epoxy compounds
-
- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08G—MACROMOLECULAR COMPOUNDS OBTAINED OTHERWISE THAN BY REACTIONS ONLY INVOLVING UNSATURATED CARBON-TO-CARBON BONDS
- C08G59/00—Polycondensates containing more than one epoxy group per molecule; Macromolecules obtained by polymerising compounds containing more than one epoxy group per molecule using curing agents or catalysts which react with the epoxy groups
- C08G59/18—Macromolecules obtained by polymerising compounds containing more than one epoxy group per molecule using curing agents or catalysts which react with the epoxy groups ; e.g. general methods of curing
- C08G59/40—Macromolecules obtained by polymerising compounds containing more than one epoxy group per molecule using curing agents or catalysts which react with the epoxy groups ; e.g. general methods of curing characterised by the curing agents used
- C08G59/50—Amines
- C08G59/5033—Amines aromatic
-
- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
- C08J5/00—Manufacture of articles or shaped materials containing macromolecular substances
- C08J5/04—Reinforcing macromolecular compounds with loose or coherent fibrous material
- C08J5/0405—Reinforcing macromolecular compounds with loose or coherent fibrous material with inorganic fibres
- C08J5/042—Reinforcing macromolecular compounds with loose or coherent fibrous material with inorganic fibres with carbon fibres
-
- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
- C08J5/00—Manufacture of articles or shaped materials containing macromolecular substances
- C08J5/04—Reinforcing macromolecular compounds with loose or coherent fibrous material
- C08J5/046—Reinforcing macromolecular compounds with loose or coherent fibrous material with synthetic macromolecular fibrous material
-
- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
- C08J5/00—Manufacture of articles or shaped materials containing macromolecular substances
- C08J5/04—Reinforcing macromolecular compounds with loose or coherent fibrous material
- C08J5/10—Reinforcing macromolecular compounds with loose or coherent fibrous material characterised by the additives used in the polymer mixture
-
- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
- C08L53/00—Compositions of block copolymers containing at least one sequence of a polymer obtained by reactions only involving carbon-to-carbon unsaturated bonds; Compositions of derivatives of such polymers
-
- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
- C08L63/00—Compositions of epoxy resins; Compositions of derivatives of epoxy resins
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- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
- C08J2363/00—Characterised by the use of epoxy resins; Derivatives of epoxy resins
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- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
- C08J2363/00—Characterised by the use of epoxy resins; Derivatives of epoxy resins
- C08J2363/02—Polyglycidyl ethers of bis-phenols
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- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
- C08J2377/00—Characterised by the use of polyamides obtained by reactions forming a carboxylic amide link in the main chain; Derivatives of such polymers
-
- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08K—Use of inorganic or non-macromolecular organic substances as compounding ingredients
- C08K2201/00—Specific properties of additives
- C08K2201/014—Additives containing two or more different additives of the same subgroup in C08K
-
- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
- C08L2207/00—Properties characterising the ingredient of the composition
- C08L2207/53—Core-shell polymer
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- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
- C08L51/00—Compositions of graft polymers in which the grafted component is obtained by reactions only involving carbon-to-carbon unsaturated bonds; Compositions of derivatives of such polymers
- C08L51/04—Compositions of graft polymers in which the grafted component is obtained by reactions only involving carbon-to-carbon unsaturated bonds; Compositions of derivatives of such polymers grafted on to rubbers
Definitions
- the present invention relates to an epoxy resin composition for fiber-reinforced composite materials, a fiber-reinforced composite material using the same, and a method for producing a fiber-reinforced composite material.
- Fiber-reinforced composite materials which consist of reinforcing fibers and matrix resins, can be designed to take advantage of the advantages of reinforcing fibers and matrix resins. .
- thermosetting resins epoxy resins, unsaturated polyester resins, vinyl ester resins, phenol resins, bismaleimide resins, cyanate resins, etc. are used.
- the prepreg method is a method in which a prepreg obtained by impregnating reinforcing fibers with an epoxy resin composition is laminated in a desired shape and heated to obtain a molded product.
- This prepreg method is suitable for the production of fiber-reinforced composite materials with high material strength required for structural materials such as aircraft and automobiles, but it requires many processes such as prepreg preparation and lamination. Therefore, it can only be produced in small quantities and is not suitable for mass production, which poses a problem of productivity.
- the RTM method is a method in which a liquid epoxy resin composition is injected into a reinforcing fiber base material placed in a heated mold, impregnated, and heat-cured in the mold to obtain a molded product.
- a one-component or two-component epoxy resin composition is used as the liquid epoxy resin composition.
- a one-liquid type epoxy resin composition is an epoxy resin composition in which all components including an epoxy resin and a curing agent are premixed together.
- the composition is called a two-component epoxy resin composition.
- a one-component epoxy resin composition is often used.
- a one-liquid type epoxy resin composition In order to apply a one-liquid type epoxy resin composition to a huge structural material such as an aircraft main wing and tail wing, it is required to simultaneously satisfy the following two conditions.
- the resin viscosity during resin injection into the reinforcing fiber base material must be kept low for a long time. In some cases, the temperature rise rate is slow, so even in that case, it is possible to impart the high level of physical properties (heat resistance, high compressive strength, impact resistance, durability) required for structural material applications to fiber reinforced composite materials. is required.
- Patent Document 1 a one-part epoxy resin composition containing methylenebis(3-chloro-2,6-diethylaniline) (M-CDEA) as a curing agent has been disclosed, which suppresses the increase in viscosity for a long time.
- Patent Document 2 a one-liquid type epoxy resin composition in which a fluorene amine curing agent is partially dispersed as a solid is disclosed, and a method for suppressing an increase in viscosity for a long time has been proposed.
- the fluorene amine curing agent dispersed as a part of the solid may aggregate, and the fluorene amine curing agent may not adhere to the reinforcing fiber base material.
- this agglomerate may be filtered out by the base material, or the fluorene amine curing agent has a very high melting point of 201°C, and may remain partially melted even at a high temperature of 180°C, resulting in poor curing. There is a problem that heat resistance is not expressed.
- Patent Documents 3 and 4 described above enable sufficiently high-speed curing, sufficiently cure the resin after molding, and can impart high heat resistance and high mechanical properties to the fiber-reinforced composite material. If the temperature rise rate is slow, the surface of the binder that connects the reinforcing fiber base material cannot be melted into the resin, and the adhesion between the resin and the binder is poor, resulting in sufficient compressive strength and compressive strength after impact for fiber-reinforced composite materials. , there is a problem that microcrack resistance is not expressed.
- the object of the present invention is to maintain a low viscosity for a long time during resin injection into a reinforcing fiber base material, and to achieve a high level of physical properties (heat resistance) required for structural material applications even when the temperature rise rate during heat curing is slow. , high compressive strength, impact resistance and durability) to fiber-reinforced composite materials. Furthermore, by using such an epoxy resin composition, it is intended to provide a fiber-reinforced composite material excellent in glass transition temperature of the cured resin, 0° compressive strength under wet heat, compressive strength after impact, and microcrack resistance. .
- the epoxy resin composition for fiber-reinforced composite materials of the present invention has the following configuration. That is, [A] tetraglycidyldiaminodiphenylmethane is contained in 70% by mass or more and 90% by mass or less in 100% by mass of the total epoxy resin component, and [B] bisphenol F type epoxy resin is included in 100% by mass of the total epoxy resin component. 10% by mass or more and 30% by mass or less, and [C] 4,4'-methylenebis(3-chloro-2,6-diethylaniline) and [D]4,4'-methylenebis(3,3',5, 5′-tetraisopropylaniline) for fiber-reinforced composite materials.
- the fiber-reinforced composite material of the present invention includes the cured epoxy resin composition for fiber-reinforced composite materials of the present invention and a reinforcing fiber base material.
- the present invention it is possible to maintain a low viscosity for a long time during resin injection into a reinforcing fiber base material, and achieve a high level of physical properties (heat resistance, high It is possible to provide an epoxy resin composition for fiber-reinforced composite materials that can impart compressive strength, impact resistance, and durability to fiber-reinforced composite materials.
- the epoxy resin composition for a fiber-reinforced composite material of the present invention contains [A] tetraglycidyldiaminodiphenylmethane in an amount of 70% by mass or more and 90% by mass or less in 100% by mass of the total epoxy resin components, and [B] bisphenol F type epoxy 10% by mass or more and 30% by mass or less of a resin in 100% by mass of the total epoxy resin component, and [C]4,4'-methylenebis(3-chloro-2,6-diethylaniline) and [D]4, Includes 4'-methylenebis(3,3',5,5'-tetraisopropylaniline).
- the above components may be simply referred to as component [A], component [B], component [C], and component [D].
- the epoxy resin composition for fiber-reinforced composite materials may be simply referred to as an epoxy resin composition.
- the epoxy resin composition containing the above parts by mass of the component [A] and the component [B] and containing the component [C] and the component [D]
- resin injection into the reinforcing fiber base material which was difficult with conventional technology, can be performed.
- the resin viscosity inside maintains low viscosity for a long time, and even when the temperature rise rate during heat curing is slow, the high level of physical properties (heat resistance, high compressive strength, impact resistance, durability) required for structural material applications is achieved. It can be applied to fiber reinforced composite materials.
- Component [A] in the present invention is tetraglycidyldiaminodiphenylmethane.
- Component [A] is a component necessary for imparting high heat resistance and mechanical properties to the cured epoxy resin and fiber-reinforced composite material.
- the tetraglycidyldiaminodiphenylmethane of component [A] means N,N,N',N'-tetraglycidyldiaminodiphenylmethane, or derivatives or isomers thereof.
- N,N,N',N'-tetraglycidyl-4,4'-diaminodiphenylmethane N,N,N',N'-tetraglycidyl-3,3'-dimethyl-4,4'-diaminodiphenylmethane , N,N,N′,N′-tetraglycidyl-3,3′-diethyl-4,4′-diaminodiphenylmethane, N,N,N′,N′-tetraglycidyl-3,3′-diisopropyl-4 ,4'-diaminodiphenylmethane, N,N,N',N'-tetraglycidyl-3,3'-di-t-butyl-4,4'-diaminodiphenylmethane, N,N,N',N'-tetra glycidyl-3,3'-dimethyl-5,5'-die
- the component [A] in the present invention must be contained in an amount of 70% by mass or more and 90% by mass or less in 100% by mass of the total epoxy resin component.
- 70% by mass or more of component [A] is contained in 100% by mass of all epoxy resin components, the cured epoxy resin exhibits high heat resistance, and the 0° compressive strength of the fiber-reinforced composite material when wet and heated is improves.
- the component [A] is contained in an amount of 90% by mass or less, the viscosity of the epoxy resin composition at the resin impregnation temperature is reduced, and the impregnating property of the reinforcing fiber substrate is improved.
- cured material refers to the hardened
- the component [B] in the present invention is a bisphenol F type epoxy resin.
- Component [B] is a component necessary for reducing the viscosity of the epoxy resin composition at the resin impregnation temperature and improving the impregnating properties of the reinforcing fiber base material.
- component [B] is a component necessary for imparting high mechanical properties to the cured epoxy resin and fiber-reinforced composite material.
- the bisphenol F type epoxy resin of component [B] has a structure in which two phenolic hydroxyl groups of bisphenol F are glycidylized.
- the resin viscosity ⁇ (mPa ⁇ s) at 50°C of component [B] preferably satisfies 1000 ⁇ 10000.
- ⁇ is 1000 mPa ⁇ s or more, the viscosity at the resin injection temperature does not become too low, and impregnation due to pits generated by entrainment of air during injection into the reinforcing fiber base material is less likely to occur.
- the epoxy resin composition has high reactivity at the resin injection temperature, the viscosity increases during the injection process, impregnating the impregnating properties is reduced, resulting in the formation of non-impregnated parts, and the molding takes a long time.
- the resin viscosity ⁇ (mPa ⁇ s) satisfies 1000 ⁇ 8000.
- examples of commercially available resins having a resin viscosity ⁇ (mPa s) satisfying the above range include “EPICLON (registered trademark)” 830 (manufactured by DIC Corporation) and “Araldite (registered trademark)” GY282 (Huntsman Japan).
- the resin viscosity ⁇ (mPa ⁇ s) in the present invention is measured using a Brookfield viscometer in accordance with JIS Z8803 (1991) "Viscosity measurement method using cone-plate rotary viscometer".
- Commercially available products of alkyl-substituted tetramethylbisphenol F-type epoxy resin include “Epototh (registered trademark)” YSLV-80XY (Nippon Steel & Sumikin Chemical Co., Ltd.).
- the component [B] in the present invention must be contained in an amount of 10% by mass or more and 30% by mass or less in 100% by mass of the total epoxy resin component.
- component [B] When 10 parts by mass or more of component [B] is contained in 100% by mass of all epoxy resin components, the viscosity of the epoxy resin composition at the resin impregnation temperature is reduced, the impregnation of the reinforcing fiber base material is improved, and the Impregnation can be prevented, and high toughness and elastic modulus are exhibited in cured epoxy resins.
- component [B] is 30 mass % or less, high heat resistance is exhibited. From this point of view, the content of component [B] is preferably in the range of 10% by mass or more and 25% by mass or less in 100% by mass of the total epoxy resin component.
- the epoxy resin composition for fiber-reinforced composite materials of the present invention may contain an epoxy resin other than component [A] and component [B] as long as it is 20% by mass or less based on 100% by mass of the total epoxy resin component.
- Epoxy resins other than component [A] and component [B] include bisphenol-type epoxy resins other than component [B], phenol novolac-type epoxy resins, cresol novolak-type epoxy resins, resorcinol-type epoxy resins, and phenol aralkyl-type epoxy resins.
- Epoxy resins other than component [A] and component [B] may be contained in one type or in two or more types.
- epoxy resins other than component [A] and component [B] include bisphenol A diglycidyl ether, tetrabromobisphenol A diglycidyl ether, bisphenol AD diglycidyl ether, 2,2′,6,6 '-Tetramethyl-4,4'-biphenol diglycidyl ether, 9,9-bis(4-hydroxyphenyl)fluorene diglycidyl ether, tris(p-hydroxyphenyl)methane triglycidyl ether, tetrakis(p-hydroxy phenyl)ethane tetraglycidyl ether, phenol novolac glycidyl ether, cresol novolac glycidyl ether, glycidyl ether of condensate of phenol and dicyclopentadiene, glycidyl ether of biphenylaralkyl resin, triglycidyl isocyanurate, 5-ethyl-1,3
- bisphenol-type epoxy resins other than the component [B] are preferably used because they tend to contribute to an excellent balance of toughness and heat resistance of cured epoxy resins.
- liquid bisphenol type epoxy resins are preferably used as epoxy resins other than component [A] and component [B] because they contribute excellently to impregnating reinforcing fibers.
- “liquid” means that the viscosity at 25°C is 1000 Pa ⁇ s or less.
- solid means that the liquid has no fluidity or extremely low fluidity at 25°C, and specifically has a viscosity of more than 1000 Pa ⁇ s at 25°C.
- the viscosity is measured according to JIS Z8803 (1991) "Viscosity measurement method using cone-flat rotary viscometer", E-type viscometer equipped with a standard cone rotor (1°34' ⁇ R24) (for example, ) Measured using Tokimec TVE-30H).
- the bisphenol-type epoxy resin excluding component [B] is a bisphenol compound other than bisphenol F in which two phenolic hydroxyl groups are glycidylized.
- Examples of bisphenol type epoxy resins other than component [B] include bisphenol A type epoxy resins, bisphenol AD type epoxy resins, bisphenol S type epoxy resins, etc.
- the bisphenol compound portion of these bisphenol type epoxy resins is halogen-substituted. , alkyl-substituted ones, hydrogenated ones, and the like.
- the bisphenol-type epoxy resin not only a monomer but also a high molecular weight substance having a plurality of repeating units can be suitably used. From the viewpoint of the balance between the toughness and heat resistance of the cured epoxy resin, the content of the bisphenol-type epoxy resin other than the component [B] should be 20% by mass or less in 100% by mass of the total epoxy resin component. is preferred.
- bisphenol A type epoxy resins include "jER (registered trademark)” 825, “jER (registered trademark)” 826, “jER (registered trademark)” 827, “jER (registered trademark)” 828, “jER ( Registered trademark)”834, “jER (registered trademark)” 1001, “jER (registered trademark)” 1002, “jER (registered trademark)” 1003, “jER (registered trademark)” 1004, “jER (registered trademark)” 1004AF , “jER (registered trademark)” 1007, “jER (registered trademark)” 1009 (manufactured by Mitsubishi Chemical Corporation), “EPICLON (registered trademark)” 850 (manufactured by DIC Corporation), “Epotote (registered trademark) “YD-128 (manufactured by Nippon Steel & Sumikin Chemical Co., Ltd.), “DER (registered trademark)”-331, “DER (registered trademark)
- Component [C] in the present invention is 4,4'-methylenebis(3-chloro-2,6-diethylaniline).
- Component [C] is a component necessary to keep the resin viscosity low for a long time during injection of the resin into the reinforcing fiber base material and to impart high mechanical properties to the cured epoxy resin and fiber-reinforced composite material.
- Commercial products of such 4,4'-methylenebis(3-chloro-2,6-diethylaniline) include "Lonza Cure (registered trademark)" M-CDEA (manufactured by Lonza Co., Ltd.).
- the component [C] in the present invention is preferably contained in an amount of 60% by mass or more and 90% by mass or less in 100% by mass of all curing agent components.
- the component [C] is contained in an amount of 60% by mass or more in 100% by mass of the total curing agent component, the reactivity of the epoxy resin composition tends to be moderately suppressed, and the resin during resin injection into the reinforcing fiber base material Viscosity becomes easy to keep low viscosity especially for a long time.
- the binder that connects the reinforcing fiber base material does not melt excessively in the resin when the temperature rise rate during heat curing is slow, and the binder shape is easily maintained.
- the content of component [C] is more preferably in the range of 70% by mass or more and 90% by mass or less in 100% by mass of the total curing agent components.
- Component [D] in the present invention is 4,4'-methylenebis(3,3',5,5'-tetraisopropylaniline).
- Component [D] is a component necessary for imparting high heat resistance and mechanical properties to the cured epoxy resin and fiber-reinforced composite material.
- Commercially available products of such 4,4'-methylenebis(3,3',5,5'-tetraisopropylaniline) include "Lonza Cure (registered trademark)" M-DIPA (manufactured by Lonza Co., Ltd.).
- Component [D] in the present invention is preferably contained in an amount of 5% by mass or more and 40% by mass or less in 100% by mass of the total curing agent component.
- component [D] is contained in an amount of 5% by mass or more in 100% by mass of all curing agent components, high heat resistance tends to be exhibited.
- the content is 40% by mass or less, the surface layer of the binder that connects the reinforcing fiber base material melts into the resin when the temperature rise rate during heat curing is slow, and the adhesion between the resin and the binder tends to be good. Sufficient compressive strength, post-impact compressive strength, and microcrack resistance are likely to develop. From this point of view, the content of component [D] is more preferably in the range of 5% by mass or more and 30% by mass or less based on 100% by mass of the total curing agent components.
- the epoxy resin composition for fiber-reinforced composite materials of the present invention preferably further contains [E]4,4'-methylenebis(2-isopropyl-6-methylaniline).
- [E]4,4'-methylenebis(2-isopropyl-6-methylaniline) may be simply referred to as component [E].
- component [E] Including the component [E] makes it easier for the epoxy resin cured product and the fiber-reinforced composite material to obtain higher heat resistance and higher mechanical properties.
- Commercially available products of such 4,4'-methylenebis(2-isopropyl-6-methylaniline) include "Lonza Cure (registered trademark)" M-MIPA (manufactured by Lonza Co., Ltd.).
- the content of component [E] is preferably 5% by mass or more and 20% by mass or less in 100% by mass of the total curing agent component.
- component [E] is contained in an amount of 5% by mass or more in 100% by mass of the total curing agent components, the heat resistance and compressive strength of the fiber-reinforced composite material are likely to be improved.
- the content is 20% by mass or less, even if the uniform epoxy resin composition in which the component [E] is dissolved is stored frozen for a long period of time, the component [E] is less likely to precipitate, resulting in excellent handleability.
- high-speed curability at a high temperature of 180° C. is likely to be exhibited. From this point of view, the content of component [E] is more preferably 5% by mass or more and 15% by mass or less in 100% by mass of the total curing agent components.
- the epoxy resin composition for fiber-reinforced composite materials of the present invention may contain a compound having an active group capable of reacting with the epoxy resin as a curing agent other than component [C], component [D], and component [E]. good.
- active groups that can react with epoxy resins include amino groups and acid anhydride groups. The higher the storage stability of the epoxy resin composition, the better.
- liquid curing agents are highly reactive. It is preferably solid.
- the curing agents other than component [C], component [D] and component [E] are preferably aromatic amines.
- curing agents other than component [C], component [D] and component [E] preferably have 1 to 4 phenyl groups in the molecule.
- the elastic modulus of the resin is improved, which can contribute to the improvement of mechanical properties. More preferably, it is an aromatic polyamine compound that is a phenyl group having an amino group at the end.
- aromatic polyamine compounds include metaphenylenediamine, diaminodiphenylmethane, diaminodiphenylsulfone, metaxylylenediamine, diphenyl-p-dianiline, alkyl-substituted derivatives thereof, and isomers having different amino group positions. body, etc.
- These curing agents can be used alone or in combination of two or more.
- diaminodiphenylmethane and diaminodiphenylsulfone are preferable from the viewpoint of imparting high heat resistance to the cured epoxy resin.
- curing agents for aromatic polyamine compounds include Seikacure S (manufactured by Wakayama Seika Kogyo Co., Ltd.), MDA-220 (manufactured by Mitsui Chemicals, Inc.), “jER Cure (registered trademark)” W (Mitsubishi Chemical Co., Ltd.), and 3,3′-DAS (manufactured by Mitsui Chemicals, Inc.), “Lonza Cure (registered trademark)” M-DEA (manufactured by Lonza Co., Ltd.), “Kayahard (registered trademark)” AA (PT) (manufactured by Nippon Kayaku Co., Ltd.) and "Lonza Cure (registered trademark)” DETDA 80 (manufactured by Lonza Co., Ltd.).
- the epoxy resin composition for fiber-reinforced composite materials of the present invention contains other components such as a curing accelerator, a plasticizer, a dye, a pigment, an inorganic filler, an antioxidant, an ultraviolet absorber, a coupling agent, and a surfactant. etc. can be included as needed.
- the epoxy resin composition for fiber-reinforced composite materials of the present invention is a composition containing component [A], component [B], component [C], and component [D] immediately before injection impregnation into the reinforcing fiber base material.
- component [A], component [B], component [C], and component [D] immediately before injection impregnation into the reinforcing fiber base material.
- Good, during storage it may be stored as a single composition containing all components, or may be stored as a plurality of compositions containing arbitrarily selected components.
- When storing as multiple compositions for example, store as two compositions, an epoxy base liquid containing component [A] and component [B], and a curing agent group containing component [C] and component [D].
- compositions containing all the components by mixing the epoxy base liquid and the curing agent group immediately before injecting and impregnating the reinforcing fiber base material.
- the combination of components contained in each composition can be arbitrarily selected.
- the combination of components contained in each composition is, from the viewpoint of preventing thickening due to the curing reaction, the epoxy resin component [A] and component [B] and the curing agent. It is preferable to include a certain component [C] and component [D] in separate compositions.
- H/E which is the ratio of the total number of epoxy groups (E) contained in the epoxy resin to the total number (H) of active hydrogens of the amine compound contained in the curing agent, is 1.1 or more and 1.4 or less. is preferred. H/E is more preferably 1.1 or more and 1.3 or less. When H/E is 1.1 or more, the effect of improving the plastic deformation ability of the cured epoxy resin is likely to be obtained. Moreover, when H/E is 1.4 or less, it becomes easy to express high heat resistance.
- the total content of components [A] to [D] is preferably 70 to 100% by mass because the effects of the present invention are manifested remarkably. , more preferably 80 to 100% by mass.
- the epoxy resin composition for fiber-reinforced composite materials of the present invention may contain core-shell rubber particles.
- Core-shell rubber particles are excellent in that they tend to impart high toughness to fiber-reinforced composite materials.
- core-shell rubber particles refer to particles in which a particulate core part mainly composed of a polymer such as crosslinked rubber is coated with a part or the whole of the core surface by a method such as graft polymerization of a polymer different from the core part. means
- components constituting the core portion of the core-shell rubber particles include polymers polymerized from one or more selected from conjugated diene-based monomers, acrylic acid ester-based monomers, and methacrylic acid ester-based monomers, or silicone resins. be done.
- conjugated diene-based monomers include butadiene, isoprene, and chloroprene.
- the polymer used as the component constituting the core portion is preferably a crosslinked polymer composed of one or more of these conjugated diene monomers.
- butadiene since the resulting polymer has good properties and is easy to polymerize, it is preferable to use butadiene as such a conjugated diene-based monomer. It is preferably a polymerized polymer.
- the shell portion of the core-shell rubber particles is preferably graft-polymerized to the core portion and chemically bonded to the polymer particles forming the core portion.
- components constituting such a shell portion include polymers polymerized from one or more selected from (meth)acrylic acid esters, aromatic vinyl compounds, and the like.
- the components constituting the shell portion include the components contained in the epoxy resin composition for fiber-reinforced composite materials of the present invention, that is, the epoxy resin or a functional agent that reacts with the curing agent thereof. A group is preferably introduced.
- Such a functional group include, for example, hydroxyl groups, carboxyl groups, epoxy groups, and the like.
- an epoxy group is preferable because it enhances the affinity between the shell component and the epoxy resin composition of the present invention, and enables the expression of good dispersibility. That is, the core-shell rubber particles are preferably core-shell rubber particles containing an epoxy group in the shell portion.
- one or a plurality of components such as acrylic acid esters and methacrylic acid esters containing such a functional group are used as a part of the monomer core.
- a method such as graft polymerization on the surface can be mentioned.
- the core-shell rubber particles preferably have a volume average particle diameter of 50 nm or more and 300 nm or less, more preferably 50 nm or more and 150 nm or less.
- the volume average particle size is measured using a Nanotrack particle size distribution analyzer (manufactured by Nikkiso Co., Ltd., dynamic light scattering method).
- a Nanotrack particle size distribution analyzer manufactured by Nikkiso Co., Ltd., dynamic light scattering method.
- a thin section of the epoxy resin cured material prepared with a microtome is observed with a TEM, and image processing software is used from the obtained TEM image. to measure the volume average particle size. In this case, it is necessary to use an average value of at least 100 particles.
- the volume average particle diameter is 50 nm or more, the specific surface area of the core-shell rubber particles is moderately small, which is advantageous in terms of energy, so aggregation is less likely to occur and the effect of improving toughness is high.
- the volume average particle size is 300 nm or less, the distance between the core-shell rubber particles is moderately small, and the effect of improving toughness is high.
- the epoxy resin composition for a fiber-reinforced composite material of the present invention contains core-shell rubber particles having an epoxy group in the shell portion, and the volume-average particle diameter of the core-shell rubber particles is in the range of 50 nm or more and 300 nm or less. preferable. That is, the epoxy resin composition for a fiber-reinforced composite material of the present invention further comprises [F] core-shell rubber particles having an epoxy group in the shell portion and having a volume average particle diameter in the range of 50 nm or more and 300 nm or less. more preferred.
- [F] core-shell rubber particles having an epoxy group in the shell portion and having a volume average particle diameter within the range of 50 nm or more and 300 nm or less may be simply referred to as component [F].
- component [F] core-shell rubber particles that satisfy these conditions, it becomes easier to disperse the particles uniformly and well in the epoxy resin composition, and it becomes easier to exhibit an excellent effect of improving toughness. .
- core-shell rubber particles there are no particular restrictions on the method for producing the core-shell rubber particles, and those produced by known methods can be used.
- Commercially available core-shell rubber particles include, for example, "Paraloid (registered trademark)” EXL-2655 (manufactured by Rohm & Haas) composed of a butadiene/alkyl methacrylate/styrene copolymer, and an acrylic acid ester/methacrylic acid ester copolymer.
- a core layer of a glassy polymer having a glass transition temperature of room temperature or higher such as Staphyloid IM-601 and IM-602 (manufactured by Ganz Kasei Co., Ltd.) is covered with an intermediate layer of a rubbery polymer having a low Tg
- core-shell rubber particles having a three-layer structure covered with a shell layer can also be used.
- these core-shell rubber particles are taken out as a lump and pulverized to be treated as powder, and the powdery core-shell rubber is often dispersed again in the thermosetting resin composition.
- this method has the problem that it is difficult to stably disperse the particles in a non-aggregated state, that is, in the state of primary particles.
- core-shell rubber particles should not be taken out in bulk form from the production process of core-shell rubber particles, but should be finally handled in the form of a masterbatch in which primary particles are dispersed in one component of a thermosetting resin, such as an epoxy resin.
- a preferable dispersion state can be obtained by using a material capable of Such core-shell rubber particles that can be handled in a masterbatch state can be produced, for example, by the method described in any one of Examples 1 to 3 of JP-A-2004-315572.
- a suspension in which core-shell rubber particles are dispersed is obtained by polymerizing core-shell rubber in an aqueous medium represented by emulsion polymerization, dispersion polymerization, and suspension polymerization.
- the suspension is mixed with an organic solvent partially soluble in water, such as a ketone solvent such as acetone or methyl ethyl ketone, or an ether solvent such as tetrahydrofuran or dioxane, and then mixed with a water-soluble electrolyte such as sodium chloride or chloride.
- An organic solvent layer and an aqueous layer are phase-separated by contacting with potassium, and an organic solvent in which core-shell rubber particles are dispersed is obtained by separating and removing the aqueous layer. Then, after mixing the epoxy resin, the organic solvent is removed by evaporation to obtain a masterbatch in which the core-shell rubber particles are dispersed in the epoxy resin in the form of primary particles.
- a masterbatch in which the core-shell rubber particles are dispersed in the epoxy resin in the form of primary particles.
- Kane Ace registered trademark
- the content of component [F] is preferably 1 part by mass or more and 10 parts by mass or less, and 1 part by mass or more and 8 parts by mass or less with respect to 100 parts by mass of the total epoxy resin component. It is more preferable to have When the content is 1 part by mass or more, it is easy to obtain a highly tough epoxy resin cured product. Further, when the content is 10 parts by mass or less, a cured epoxy resin product having a high elastic modulus is likely to be obtained, and the dispersibility of the core-shell rubber particles in the resin is likely to be good. Even if the core-shell rubber particles have epoxy groups, the core-shell rubber particles do not fall under the epoxy resin component.
- a generally used dispersion method can be used. Examples thereof include a method using a three-roll mill, ball mill, bead mill, jet mill, homogenizer, and rotation/revolution mixer. Also, a method of mixing the core-shell rubber particle-dispersed epoxy masterbatch described above can be preferably used. However, even if the particles are dispersed in the state of primary particles, reaggregation may occur due to excessive heating or reduction in viscosity.
- the temperature/viscosity within a range in which the core-shell rubber particles do not reaggregate.
- the viscosity of the composition may decrease and aggregation may occur, so it is preferable to knead at a temperature lower than that.
- the temperature can exceed 150° C. because reaggregation is prevented due to gelation during the temperature rise.
- the epoxy resin composition for fiber-reinforced composite materials of the present invention has a resin viscosity ⁇ (mPa ⁇ s) after 240 minutes at a constant temperature of 120°C, which is obtained by isothermal measurement with an E-type viscometer, and satisfies 20 ⁇ ⁇ ⁇ 200. is preferred.
- ⁇ is 20 mPa ⁇ s or more, the viscosity at the resin injection temperature does not become too low, and impregnation due to pits caused by entrainment of air during injection into the reinforcing fiber base material is less likely to occur.
- the epoxy resin composition has high reactivity at the resin injection temperature, the viscosity increases during the injection process, impregnating the impregnating properties is reduced, resulting in the formation of non-impregnated parts, and the molding takes a long time.
- ⁇ is 200 mPa ⁇ s or less, the viscosity at the resin injection temperature is sufficiently low, so that impregnation into the reinforcing fiber base material is good, and non-impregnation is less likely to occur. From this point of view, it is more preferable to satisfy 20 ⁇ 180.
- the viscosity in the present invention is measured in accordance with JIS Z8803 (1991) "Method for measuring viscosity with a cone-plate rotary viscometer", E-type viscometer equipped with a standard cone rotor (1°34' x R24) (Tokyo Keiki It is measured using a TVE-30H manufactured by Co., Ltd. at a rotational speed of 50 rpm.
- the epoxy resin composition for a fiber-reinforced composite material of the present invention preferably has a gelling temperature in the range of 170° C. or higher and 185° C. or lower when heated from 70° C. at a heating rate of 0.5° C./min.
- gelation of the epoxy resin composition means that the reaction between the epoxy resin and the curing agent in the resin progresses and the fluidity is lost.
- thermosetting measuring device such as ATD-1000 (manufactured by Alpha Technologies Co., Ltd.)
- the dynamic viscoelasticity of the epoxy resin composition was measured by heating from 70 ° C. at a temperature increase rate of 0.5 ° C./min.
- the gelation temperature When the gelation temperature is 170° C. or higher, the gelation temperature tends to be higher than the melting point of the binder that connects the reinforcing fiber base materials. When the gelation temperature is higher than the melting point of the binder, the binder that connects the reinforcing fiber base material begins to melt at a temperature lower than the gelation temperature of the epoxy resin composition.
- the epoxy resin gels and hardens, entangling the resin and polyamide molecular chains and improving the interfacial adhesive strength, making it easier to improve compressive strength, impact resistance, and microcrack resistance.
- the gelation temperature is 185° C. or lower, the gelation temperature is unlikely to be too high relative to the melting point of the binder that connects the reinforcing fiber base materials. In such a case, the binder that connects the reinforcing fiber base material does not melt too much in the resin and maintains the shape of the binder. Post-impact compressive strength is likely to develop. From this point of view, the gelling temperature is more preferably in the range of 175°C or higher and 185°C or lower.
- the epoxy resin composition for fiber-reinforced composite materials of the present invention preferably has a glass transition temperature Tg of 170°C or higher and 190°C or lower when cured at 180°C for 120 minutes.
- the heat resistance of the fiber-reinforced composite material depends on the glass transition temperature of the cured epoxy resin composition obtained by curing the epoxy resin composition. By setting the Tg to 170° C. or higher, the heat resistance of the cured epoxy resin can be easily ensured. In addition, by setting the temperature to 190° C. or less, curing shrinkage of the epoxy resin composition is suppressed, and deterioration of the surface quality of the fiber-reinforced composite material caused by the difference in thermal expansion between the epoxy resin composition and the reinforcing fiber can be easily prevented. Become.
- the glass transition temperature Tg is 175° C. or more and 190° C. or less from the relationship between heat resistance and surface quality.
- the glass transition temperature Tg of the epoxy resin cured product obtained by curing the epoxy resin composition is obtained by measurement using a dynamic viscoelasticity measurement (DMA) device. That is, using a rectangular test piece cut out from a cured resin plate, DMA measurement is performed under elevated temperature, and the temperature at the inflection point of the obtained storage elastic modulus G' is defined as Tg.
- DMA dynamic viscoelasticity measurement
- the fiber-reinforced composite material of the present invention includes the cured epoxy resin composition for fiber-reinforced composite materials of the present invention and a reinforcing fiber base material.
- an epoxy resin composition comprising an epoxy resin and a curing agent is injected into a reinforcing fiber base material placed in a heated mold, impregnated, and cured in the mold.
- the RTM method is preferably used from the viewpoint of productivity and the degree of freedom in the shape of the resulting molded product.
- a mold having a plurality of injection ports is used, and the epoxy resin composition is injected from the plurality of injection ports at the same time or sequentially with a time lag.
- a sheet-like base material such as a reinforcing fiber fabric is laminated and shaped using a hot-melt binder (tackifier), and processed into a shape similar to the desired product. preforms are often used. Both thermoplastic resins and thermosetting resins can be used as hot-melt binders.
- the form of the binder is not particularly limited, but forms such as films, tapes, long fibers, short fibers, spun yarns, woven fabrics, knitted fabrics, non-woven fabrics, nets, and particles can be employed. Among them, a particle form or a non-woven fabric form is particularly suitable for use. When the binder is in the form of particles, it is called binder particles, and when the binder is in the form of nonwoven fabric, it is called binder nonwoven fabric.
- the average particle size is preferably 10 ⁇ m or more and 500 ⁇ m or less.
- the average particle size refers to the median size.
- the average particle size of the binder particles can be measured using, for example, a laser diffraction particle size distribution meter.
- the average particle size is 10 ⁇ m or more, the adhesion strength and workability when used as a preform are likely to be improved. From this point of view, the average particle size is more preferably 30 ⁇ m or more.
- the average particle size is 500 ⁇ m or less, the reinforcing fibers are less likely to waviness when formed into a preform, and the resulting fiber-reinforced composite material tends to have improved mechanical properties. From this point of view, the average particle size is more preferably 300 ⁇ m or less.
- the average diameter of the fibers constituting the nonwoven fabric is preferably 10 ⁇ m or more and 300 ⁇ m or less.
- the average diameter is obtained by observing the cross section of the binder nonwoven fabric with a scanning electron microscope, measuring the diameters of 100 arbitrarily selected fibers, and calculating the arithmetic mean value. If the cross-sectional shape of the fiber is not perfectly circular, the minor axis is measured as its diameter. When the average diameter is 10 ⁇ m or more, the adhesion strength of the preform is likely to be improved.
- the average diameter is 300 ⁇ m or less, the reinforcing fibers of the preform are less likely to waviness, and the resulting fiber-reinforced composite material tends to have improved mechanical properties. From this point of view, the average diameter is more preferably 100 ⁇ m or less.
- the binder is attached to at least the surface of the reinforcing fiber base material and used as a reinforcing fiber base material with a binder. Further, the binder-attached reinforcing fiber base material has at least the above-described binder on its surface, and is used for a preform.
- the reinforcing fiber base material is a preform in which the reinforcing fiber base material is connected with a binder in the form of a non-woven fabric. Since the reinforcing fiber base material is a preform in which the reinforcing fiber base material is connected with a binder in the form of a non-woven fabric, the binder can be uniformly arranged on the base material. Therefore, it is particularly excellent in impregnation, and voids are extremely unlikely to occur. In addition, even if the amount of the binder attached is smaller than that of the binder in the form of particles, the effect of fixing the shape when used as a preform can be maintained at the same level. It is easy to express heat resistance and mechanical properties.
- the fiber-reinforced composite material of the present invention is a gel obtained by heating the epoxy resin composition for fiber-reinforced composite materials from 70° C. at a heating rate of 0.5° C./min in the cured product of the epoxy resin composition for fiber-reinforced composite materials.
- the curing temperature is preferably equal to or higher than the melting point of the binder that connects the reinforcing fiber base materials.
- the difference between the gelation temperature and the melting point (gelation temperature - melting point) is more preferably 1°C or more, and even more preferably 4°C or more.
- the difference between the gelling temperature and the melting point is preferably 20° C. or less, more preferably 15° C. or less.
- the binder that connects the reinforcing fiber base material begins to melt at a temperature lower than the gelation temperature of the epoxy resin composition, so the epoxy resin composition enters into the gaps between the loosened polyamide molecular chains.
- the epoxy resin gels and hardens, and the resin and polyamide molecular chains are entangled to improve the interfacial adhesive strength, and the compressive strength, impact resistance, and microcrack resistance are easily improved. Since the binder that connects the fiber base material does not melt too much in the resin and maintains the shape of the binder, it is possible to ensure a uniform interlayer thickness that allows sufficient plastic deformation in the fiber-reinforced composite material, and to develop sufficient compressive strength after impact. easier to do.
- the binder in the form of nonwoven fabric is preferably made of polyamide having a melting point of 165°C or higher and 180°C or lower.
- the melting point of the polyamide is 165°C or higher, the shape can be maintained during curing, making it easier to ensure a uniform interlayer thickness that allows sufficient plastic deformation, and because the nonwoven fabric is a continuous phase, cracks are effectively blocked. can be made easier, and the impact resistance can be easily expressed.
- the melting point of the polyamide is 180° C. or lower, the melting point of the polyamide tends to be lower than the gelling temperature of the epoxy resin composition.
- the polyamide When the melting point of the polyamide is lower than the gelling temperature of the epoxy resin composition, the polyamide begins to melt at a temperature lower than the gelling temperature of the epoxy resin composition. In this state, the epoxy resin gels and hardens, so that the resin and the polyamide molecular chains are entangled and the interfacial adhesive strength is improved, and the compressive strength, impact resistance, and microcrack resistance are further improved.
- the binder in the form of non-woven fabric is preferably attached to one or both sides of the fiber-reinforced base material.
- the amount of the binder in the form of nonwoven fabric attached to the surface of the fiber-reinforced base material is preferably 0.5 g/m 2 or more and 10 g/m 2 or less per side. More preferably, the adhesion amount is 1 g/m 2 or more and 7 g/m 2 or less.
- the adhesion amount is 0.5 g/m 2 or more, the shape of the preform tends to be easily fixed.
- the matrix resin tends to exhibit sufficient impregnating properties, and voids are less likely to occur.
- the same effect can be maintained even if the amount of adhered binder is smaller than when the form of particles is adopted.
- the adhered amount per side is 0.5 g/m 2 or more and 50 g/m 2 or less, preferably 1 g/m 2 or more and 30 g/m 2 or less.
- the adhesion amount of is preferable, in the non-woven fabric binder, the adhesion amount should be 0.5 g / m 2 or more and 10 g / m 2 or less while maintaining the same effect of fixing the shape when made into a preform. is also possible.
- a method for obtaining a preform includes, for example, a method of laminating reinforcing fiber base materials with a binder having at least the binder on the surface and fixing the shape. More specifically, for example, a binder is adhered to at least one surface of the reinforcing fiber base material by heating to form a reinforcing fiber base material with a binder, and then a plurality of the binder-attached reinforcing fiber base materials are laminated, so that at least the binder is laminated. A laminate having between the layers is obtained. There is a method of obtaining a preform having a binder at least between the laminated layers by heating and cooling this to fix the shape by fixing the binder between the base layers.
- a preform can be produced by cutting a binder-attached reinforcing fiber base material to a predetermined shape, laminating it on a mold, and applying appropriate heat and pressure.
- a pressurizing means a press can be used, or a method of enclosing with a vacuum bag film and sucking the inside with a vacuum pump to pressurize with atmospheric pressure can also be used.
- the fiber volume content of the reinforcing fibers is preferably in the range of 45% or more and 70% or less, more preferably in the range of 50% or more and 65% or less.
- the fiber volume content is 45% or more, a fiber-reinforced composite material having a higher elastic modulus and an excellent weight reduction effect can be obtained.
- it is 70% or less, a fiber-reinforced composite material can be obtained which is free from deterioration in strength due to rubbing between reinforcing fibers and which is excellent in mechanical properties such as tensile strength.
- the reinforcing fibers that make up the reinforcing fiber base material in the present invention are not particularly limited, but include glass fibers, carbon fibers, graphite fibers, aramid fibers, boron fibers, alumina fibers, silicon carbide fibers, and the like. Two or more kinds of these reinforcing fibers may be mixed and used. Among them, it is preferable to use carbon fiber or graphite fiber in order to obtain a fiber-reinforced composite material that is lighter in weight and has higher durability. In particular, in applications where there is a high demand for lightweight materials and high strength, the fiber-reinforced composite material of the present invention has excellent specific elastic modulus and specific strength. Carbon fibers are preferred.
- carbon fibers having a tensile elastic modulus of 230 GPa or more and 400 GPa or less are preferable from the viewpoint of impact resistance.
- carbon fibers having a tensile strength of 4.4 GPa or more and 6.5 GPa or less are preferable because a composite material having high rigidity and mechanical strength can be obtained.
- Tensile elongation is also an important factor, and a high-strength, high-elongation carbon fiber of 1.7% or more and 2.3% or less is preferable.
- Carbon fibers having the combined properties of a tensile modulus of at least 230 GPa, a tensile strength of at least 4.4 GPa and a tensile elongation of at least 1.7% are therefore most suitable.
- Carbon fibers include “Torayca (registered trademark)” T800G-24K, “Torayca (registered trademark)” T800S-24K, “Torayca (registered trademark)” T700G-24K, “Torayca (registered trademark)” T300- 3K, and “Torayca (registered trademark)” T700S-12K (manufactured by Toray Industries, Inc.).
- the fiber-reinforced composite material of the present invention includes the epoxy resin cured product of the epoxy resin composition for fiber-reinforced composite materials of the present invention and a reinforcing fiber base material.
- Fiber-reinforced composite materials are required to have high heat resistance and mechanical properties, especially when used in the field of aircraft.
- the glass transition temperature of the cured epoxy resin which is the matrix resin, is preferably 170° C. or higher and 190° C. or lower. By having a glass transition temperature within this range, excellent heat resistance and high mechanical properties of the epoxy resin cured product are reflected.
- the fiber-reinforced composite material of the present invention has a high H/W0° compressive strength, which is the 0° compressive strength in wet heat, preferably 1000 MPa or more, and more preferably 1100 MPa or more. can be shown.
- the post-impact compressive strength is preferably 260 MPa or more, more preferably 270 MPa or more, and can exhibit a high post-impact compressive strength.
- microcracks are minute cracks of about several tens of ⁇ m that may occur in fiber reinforced composite materials used in aircraft applications, It is known that it is likely to occur when repeatedly exposed to an environment where temperature changes are repeated.
- the matrix resin in the fiber-reinforced composite material is exposed to an atmosphere with a high temperature of about 70°C to a low temperature of about -50°C, the matrix resin itself tries to shrink, but it is surrounded by reinforcing fibers that hardly shrink.
- tensile stress thermal residual stress
- the number of microcracks is preferably less than 10, more preferably 5 or less, from the viewpoint of long-term durability of the fiber-reinforced composite material. A specific method for calculating the number of microcracks will be described later.
- the epoxy resin composition for a fiber-reinforced composite material of the present invention heated to 50° C. or higher and 130° C. or lower is placed in a mold heated to 90° C. or higher and 180° C. or lower. It is injected into the reinforcing fiber base material, impregnated, and cured in the mold.
- the epoxy resin composition for fiber-reinforced composite materials was selected from the range of 50° C. or higher and 130° C. or lower based on the relationship between the initial viscosity of the epoxy resin composition and the viscosity increase from the viewpoint of impregnation into the reinforcing fiber base material. heated to temperature before injection.
- the epoxy resin composition for fiber-reinforced composite materials of the present invention preferably has a resin viscosity of 200 mPa ⁇ s or less, more preferably 180 mPa ⁇ s or less after 240 minutes at a constant temperature of 120°C.
- viscosity measurement is performed by the method described later. If the viscosity after 240 minutes from the start of injection is higher than the above range, the impregnating properties of the epoxy resin composition may be insufficient. In addition, the resin viscosity after 240 minutes at a constant temperature of 120° C.
- the mold temperature is preferably 90° C. or higher and 180° C. or lower. To obtain a fiber-reinforced composite material with good surface quality by reducing the time required for curing and at the same time alleviating heat shrinkage after demolding by setting the mold temperature to 90° C. or higher and 180° C. or lower. can be done.
- the injection pressure of the epoxy resin composition for fiber-reinforced composite materials is usually 0.1 MPa or more and 1.0 MPa or less.
- a VaRTM (Vacuum Assist Resin Transfer Molding) method in which the inside of the mold is vacuum-sucked to inject the epoxy resin composition can also be used.
- the injection pressure of the epoxy resin composition for fiber-reinforced composite materials is preferably 0.1 MPa or more and 0.6 MPa in terms of injection time and facility economy. Also, even in the case of pressurized injection, it is preferable to evacuate the inside of the mold before injecting the epoxy resin composition for fiber-reinforced composite material, because the generation of voids can be suppressed.
- the fiber-reinforced composite material of the present invention has excellent heat resistance, high compressive strength, impact resistance, and durability, it can be used for aircraft such as fuselages, main wings, tail wings, rotor blades, fairings, cowls, doors, seats, and interior materials.
- aircraft such as fuselages, main wings, tail wings, rotor blades, fairings, cowls, doors, seats, and interior materials.
- Components, motor cases, spacecraft components such as main wings, satellite components such as structures and antennas, outer panels, chassis, aerodynamic components, automotive components such as seats, railway vehicle components such as structures and seats, ships such as hulls and seats It can be preferably used for many structural materials such as members.
- a binder was prepared according to the following manufacturing method.
- Fibers of PA-1 (melting point: 170°C) extruded from a nozzle provided with one orifice are stretched using an aspirator provided with an impact plate at the tip and compressed air, and then dispersed and collected in a wire mesh. did.
- the fiber sheet collected on the wire mesh was thermally bonded using a hot press to prepare a binder 1 in the form of a non-woven fabric.
- Binder 2 (Preparation of Binder 2) PES ("Sumika Excel (registered trademark)" 5003P, melting point: none) extruded from a nozzle provided with one orifice is spun using an aspirator with an impact plate at the tip and compressed air. After being stretched with a wire mesh, it was scattered and collected. The fiber sheet collected on the wire mesh was thermally bonded using a hot press to prepare a binder 2 in the form of a non-woven fabric.
- Binder 3 (Preparation of Binder 3) Fibers of PA-2 ("Amilan (registered trademark)" CM1001 manufactured by Toray Industries, Inc., melting point: 225°C) discharged from a nozzle provided with one orifice are passed through an aspirator provided with an impact plate at the tip and compressed air. It was then stretched using a wire mesh and collected by scattering. The fiber sheet collected on the wire mesh was thermally bonded using a heating press to prepare a binder 3 in the form of a non-woven fabric.
- PA-2 Similar (registered trademark)" CM1001 manufactured by Toray Industries, Inc., melting point: 225°C
- Binder 4 (Preparation of Binder 4) Fibers of PA-3 ("Platamid (registered trademark)" M1657 manufactured by Arkema Co., Ltd., melting point: 110°C) discharged from a nozzle provided with one orifice are passed through an aspirator provided with an impact plate at the tip and compressed air. It was then stretched using a wire mesh and collected by scattering. The fiber sheet collected on the wire mesh was thermally bonded using a heating press to prepare a binder 4 in the form of a non-woven fabric.
- PA-3 Plateamid (registered trademark)” M1657 manufactured by Arkema Co., Ltd., melting point: 110°C) discharged from a nozzle provided with one orifice are passed through an aspirator provided with an impact plate at the tip and compressed air. It was then stretched using a wire mesh and collected by scattering. The fiber sheet collected on the wire mesh was thermally bonded using a heating press to prepare a binder 4 in the form of a non-woven fabric.
- the prepared binder resin composition was frozen and pulverized with liquid nitrogen using a hammer mill (PULVERIZER, manufactured by Hosokawa Micron Corporation) using a screen with a hole size of 1 mm to obtain binder 5 in the form of particles.
- the particles were passed through sieves with an opening size of 150 ⁇ m and 75 ⁇ m, and the binder particles remaining on the sieve with an opening size of 75 ⁇ m were used for evaluation.
- the resulting binder was a carbon fiber unidirectional fabric (plain weave, warp: carbon fiber T800S-24K-10C manufactured by Toray Industries, Inc., carbon fiber basis weight: 295 g/m 2 , warp density: 7.2/25 mm, weft: glass fiber. ECE225 1/0 1Z (manufactured by Nittobo Co., Ltd., weft density 7.5/25 mm).
- the adhesion amount was 5 g/m 2 for binders 1 to 4, and 10 g/m 2 for binder 5.
- the substrate was heated using a far-infrared heater to fuse the binder, thereby obtaining a binder-attached reinforcing fiber substrate having a binder applied to one surface.
- the epoxy resin composition which had been separately heated to 120° C. in advance was injected into the mold at an injection pressure of 0.2 MPa using a resin injection device.
- the mold was heated from 120° C. to 180° C. at a rate of 0.5° C./min, and after curing at 180° C. for 2 hours, the temperature was lowered to 30° C. to obtain a fiber-reinforced composite material.
- the environmental exposure in the constant temperature and humidity chamber and the cycle in the environmental tester are defined as one block, and the cycle is repeated for 5 blocks.
- a width of 25 mm was cut from a region ⁇ 10 mm from the longitudinal center of the test piece exposed to the above environment, the cut surface was polished as an observation surface, and the observation surface was observed at a magnification of 200 using a commercially available microscope.
- the number of generated cracks was counted. From the viewpoint of long-term durability of the fiber-reinforced composite material, the number of microcracks observed by the above method is preferably less than 10, more preferably 5 or less.
- a case of 6 or more and less than 10 was rated B, and a case of 10 or more was rated C.
- Example 1 As shown in Table 1-1, 70 parts by mass of "Araldite (registered trademark)” MY721 as component [A], 30 parts by mass of "EPICLON (registered trademark)” 830 as component [B], and " 59 parts by mass of Lonzacure (registered trademark) "M-CDEA” and 25 parts by mass of "Lonzacure (registered trademark)” M-DIPA as component [D] were added and stirred at 80°C for 1 hour to prepare an epoxy resin composition. . As described above, the gelation temperature of the epoxy resin composition was measured and found to be 177°C.
- the interfacial adhesion between the binder and the resin is good and the shape of the binder is maintained, so sufficient plastic deformation is possible in the fiber-reinforced composite material. It was a particularly preferable temperature at which a uniform interlayer thickness could be ensured.
- the viscosity of the epoxy resin composition after being kept at 120° C. for 240 minutes was measured and found to be 140 mPa ⁇ s.
- a resin cured product was prepared by the method described above, and the Tg of the cured product was measured.
- a fiber-reinforced composite material was produced using this epoxy resin composition, and the 0° compressive strength under wet heat, the compressive strength after impact, and the number of microcracks were measured. , the compressive strength after impact was 280 MPa, and the number of microcracks was 5 or less.
- Examples 2-5 An epoxy resin composition was prepared in the same manner as in Example 1, except that the content of each component was changed as shown in Table 1-1. As a result of measuring the gelation temperature of the epoxy resin composition as described above, all of them were 170° C. or higher and 185° C. or lower. It was the temperature at which a uniform interlayer thickness that enables sufficient plastic deformation can be ensured. Among them, Examples 2, 3, and 5 had a temperature of 175° C. or more and 185° C. or less, which was a particularly favorable result. Next, the viscosities of the epoxy resin compositions after being kept at 120° C. for 240 minutes were measured.
- Examples 2, 3 and 5 had a viscosity of 180 mPa ⁇ s or less, which was a particularly favorable result.
- cured resins were prepared by the method described above, and the Tg of the cured products was measured.
- a fiber-reinforced composite material was produced using this epoxy resin composition, and the 0° compressive strength under wet heat, the compressive strength after impact, and the number of microcracks were measured.
- the compressive strength after impact was 260 MPa or more, and the number of microcracks was less than 10, indicating good mechanical properties and durability.
- Examples 2, 3, and 5 had a wet heat 0° compressive strength of 1100 MPa or more, a post-impact compressive strength of 270 MPa or more, and the number of microcracks of 5 or less, which were particularly favorable results.
- Example 6 As shown in Table 1-1, 80 parts by mass of "Araldite (registered trademark)” MY721 as component [A], 20 parts by mass of "EPICLON (registered trademark)” 830 as component [B], and " 52 parts by mass of "Lonzacure (registered trademark)” M-CDEA, 17 parts by mass of "Lonzacure (registered trademark)” M-DIPA as component [D], and “Lonzacure (registered trademark)” M-MIPA as component [E]. 15 parts by mass were added and stirred at 80° C. for 1 hour to prepare an epoxy resin composition. As described above, the gelling temperature of the epoxy resin composition was measured and found to be 170°C.
- the interfacial adhesion between the binder and the resin is good and the shape of the binder is maintained, so sufficient plastic deformation is possible in the fiber-reinforced composite material.
- the temperature was such that a uniform interlayer thickness could be ensured.
- a resin cured product was produced by the method described above, and the Tg of the cured product was measured to be 186° C., and the heat resistance was particularly good.
- a fiber-reinforced composite material was produced using this epoxy resin composition, and the 0° compressive strength under wet heat, the compressive strength after impact, and the number of microcracks were measured.
- the strength was 260 MPa, and the number of microcracks was 6 or more and less than 10.
- Examples 7 and 8 An epoxy resin composition was prepared in the same manner as in Example 6, except that the content of each component was changed as shown in Tables 1-1 and 1-2. As described above, as a result of measuring the gelation temperature of the epoxy resin composition, all of them were 175 ° C. or higher and 185 ° C. or lower. It was a particularly preferable temperature at which a uniform interlayer thickness capable of sufficient plastic deformation could be ensured. Next, the viscosities of the epoxy resin compositions after being kept at 120° C. for 240 minutes were measured, and all of them were 180 mPa ⁇ s or less, and the impregnating properties into reinforcing fibers were particularly good.
- cured resins were prepared by the method described above, and the Tg of the cured products was measured. Furthermore, a fiber-reinforced composite material was produced using this epoxy resin composition, and the 0° compressive strength under wet heat, the compressive strength after impact, and the number of microcracks were measured. The compressive strength after impact was 270 MPa or more, and the number of microcracks was 5 or less.
- Example 9 An epoxy resin composition was prepared in the same manner as in Example 7, except that "Araldite (registered trademark)" GY282 was used as component [B]. As described above, the gelation temperature of the epoxy resin composition was measured and found to be 175°C. The interfacial adhesion between the binder and the resin is good and the shape of the binder is maintained, so sufficient plastic deformation is possible in the fiber-reinforced composite material. It was a particularly preferable temperature at which a uniform interlayer thickness could be ensured. Next, as a result of measuring the viscosity of the epoxy resin composition after keeping it at 120° C.
- a resin cured product was prepared by the method described above, and the Tg of the cured product was measured. Furthermore, a fiber-reinforced composite material was produced using this epoxy resin composition, and the 0° compressive strength under wet heat, the compressive strength after impact, and the number of microcracks were measured. , the compressive strength after impact was 270 MPa, and the number of microcracks was 5 or less.
- Example 10 An epoxy resin composition was prepared in the same manner as in Example 7, except that "Lonzacure (registered trademark)" M-DEA was used instead of component [E]. As described above, the gelation temperature of the epoxy resin composition was measured and found to be 176°C. The interfacial adhesion between the binder and the resin is good and the shape of the binder is maintained, so sufficient plastic deformation is possible in the fiber-reinforced composite material. It was a particularly preferable temperature at which a uniform interlayer thickness could be ensured. Next, as a result of measuring the viscosity of the epoxy resin composition after keeping it at 120° C. for 240 minutes, it was found to be 160 mPa ⁇ s.
- a resin cured product was prepared by the method described above, and the Tg of the cured product was measured. Furthermore, a fiber-reinforced composite material was produced using this epoxy resin composition, and the 0° compressive strength under wet heat, the compressive strength after impact, and the number of microcracks were measured. , the compressive strength after impact was 270 MPa, and the number of microcracks was 5 or less.
- Example 11-13 An epoxy resin composition was prepared in the same manner as in Example 2, except that the content of each component and H/E were changed as shown in Table 1-2. As a result of measuring the gelation temperature of the epoxy resin composition as described above, all of them were 170° C. or higher and 185° C. or lower. It was the temperature at which a uniform interlayer thickness that enables sufficient plastic deformation can be ensured. Among them, Examples 11 and 12 had a temperature of 175° C. or higher and 185° C. or lower, which was a particularly favorable result. Next, the viscosities of the epoxy resin compositions after being kept at 120° C. for 240 minutes were measured.
- Examples 11 and 12 had a viscosity of 180 mPa ⁇ s or less, which was a particularly favorable result.
- resin cured products were produced by the method described above, and the Tg of the cured products was measured.
- Examples 11 and 12 had a temperature of 175° C. or higher, which was a particularly favorable result.
- a fiber-reinforced composite material was produced using this epoxy resin composition, and the 0° compressive strength under wet heat, the compressive strength after impact, and the number of microcracks were measured. The compressive strength after impact was 260 MPa or more, and the number of microcracks was less than 10, indicating good mechanical properties and durability.
- Example 11 has 5 or less microcracks
- Example 12 has a wet heat 0° compressive strength of 1100 MPa or more, a post-impact compressive strength of 270 MPa or more, and a microcrack count of 5 or less. This was a favorable result.
- Example 14-16 An epoxy resin composition was prepared in the same manner as in Example 7, except that the content of each component and H/E were changed as shown in Tables 1-2 and 1-3. As a result of measuring the gelation temperature of the epoxy resin composition as described above, all of them were 170° C. or higher and 185° C. or lower. It was the temperature at which a uniform interlayer thickness that enables sufficient plastic deformation can be ensured. Among them, Examples 14 and 15 had a temperature of 175° C. or more and 185° C. or less, which was a particularly favorable result. Next, the viscosities of the epoxy resin compositions after being kept at 120° C. for 240 minutes were measured.
- Examples 14 and 15 had a viscosity of 180 mPa ⁇ s or less, which was a particularly favorable result.
- resin cured products were produced by the method described above, and the Tg of the cured products was measured.
- Examples 14 and 15 had a temperature of 175° C. or higher, which was a particularly favorable result.
- a fiber-reinforced composite material was produced using this epoxy resin composition, and the 0° compressive strength under wet heat, the compressive strength after impact, and the number of microcracks were measured. The compressive strength after impact was 260 MPa or more, and the number of microcracks was less than 10, indicating good mechanical properties and durability.
- Example 14 has 5 or less microcracks
- Example 15 has a wet heat 0° compressive strength of 1140 MPa, a post-impact compressive strength of 275 MPa, and a microcrack count of 5 or less, which are particularly favorable results.
- Met the wet heat 0° compressive strength of 1140 MPa, a post-impact compressive strength of 275 MPa, and a microcrack count of 5 or less, which are particularly favorable results.
- Example 17 As shown in Table 1-3, 65 parts by mass of "Araldite (registered trademark)” MY721 as component [A], 20 parts by mass of "EPICLON (registered trademark)” 830 as component [B], and " 61 parts by mass of "Lonzacure (registered trademark)” M-CDEA, 26 parts by mass of "Lonzacure (registered trademark)” M-DIPA as component [D], and "Kane Ace (registered trademark)” MX-416 as component [F] 20 parts by mass were added and stirred at 80° C. for 1 hour to prepare an epoxy resin composition. As described above, the gelation temperature of the epoxy resin composition was measured and found to be 177°C.
- the interfacial adhesion between the binder and the resin is good and the shape of the binder is maintained, so sufficient plastic deformation is possible in the fiber-reinforced composite material. It was a particularly preferable temperature at which a uniform interlayer thickness could be ensured.
- the viscosity of the epoxy resin composition after keeping it at 120° C. for 240 minutes, it was found to be 170 mPa ⁇ s, and the impregnating property into reinforcing fibers was particularly good.
- a resin cured product was produced by the method described above, and the Tg of the cured product was measured to be 182° C., and the heat resistance was particularly good.
- a fiber-reinforced composite material was produced using this epoxy resin composition, and the 0° compressive strength under wet heat, the compressive strength after impact, and the number of microcracks were measured.
- the strength was 280 MPa, the number of microcracks was 5 or less, and the mechanical properties and durability were particularly good.
- Example 18 An epoxy resin composition was prepared in the same manner as in Example 17, except that the content of each component and the type of core-shell rubber particles were changed as shown in Table 1-3. As described above, as a result of measuring the gelation temperature of the epoxy resin composition, all of them were 175 ° C. or higher and 185 ° C. or lower. It was a particularly preferable temperature at which a uniform interlayer thickness capable of sufficient plastic deformation could be ensured. Next, the viscosities of the epoxy resin compositions after being kept at 120° C. for 240 minutes were measured. Among them, Example 19 had a value of 170 mPa ⁇ s, which was a particularly favorable result.
- cured resins were prepared by the method described above, and the Tg of the cured products was measured. Furthermore, a fiber-reinforced composite material was produced using this epoxy resin composition, and the 0° compressive strength under wet heat, the compressive strength after impact, and the number of microcracks were measured. The compressive strength after impact was 260 MPa or more, indicating good mechanical properties, and the number of microcracks was 5 or less, indicating particularly good durability. Among them, Example 18 had a compressive strength after impact of 280 MPa, which was a particularly favorable result.
- Example 20 As shown in Table 1-3, 65 parts by mass of "Araldite (registered trademark)” MY721 as component [A], 20 parts by mass of "EPICLON (registered trademark)” 830 as component [B], and " 78 parts by mass of "Lonzacure (registered trademark)” M-CDEA, 5 parts by mass of “Lonzacure (registered trademark)” M-DIPA as component [D], and “Lonzacure (registered trademark)” M-MIPA as component [E] 4 parts by mass and 20 parts by mass of "Kane Ace (registered trademark)” MX-416 as component [F] were added and stirred at 80°C for 1 hour to prepare an epoxy resin composition.
- the gelling temperature of the epoxy resin composition was measured and found to be 184°C.
- the interfacial adhesion between the binder and the resin is good and the shape of the binder is maintained, so sufficient plastic deformation is possible in the fiber-reinforced composite material. It was a particularly preferable temperature at which a uniform interlayer thickness could be ensured.
- the viscosity of the epoxy resin composition after keeping it at 120° C. for 240 minutes, it was found to be 120 mPa ⁇ s, and the impregnating property into reinforcing fibers was particularly good.
- a resin cured product was produced by the method described above, and the Tg of the cured product was measured to be 180° C., and the heat resistance was particularly good.
- a fiber-reinforced composite material was produced using this epoxy resin composition, and the 0° compressive strength under wet heat, the compressive strength after impact, and the number of microcracks were measured.
- the strength was 280 MPa, the number of microcracks was 5 or less, and the mechanical properties and durability were particularly good.
- Example 21 and 22 An epoxy resin composition was prepared in the same manner as in Example 20, except that the content of each component and the type of core-shell rubber particles were changed as shown in Table 1-4. As described above, as a result of measuring the gelation temperature of the epoxy resin composition, all of them were 175 ° C. or higher and 185 ° C. or lower. It was a particularly preferable temperature at which a uniform interlayer thickness capable of sufficient plastic deformation could be ensured. Next, the viscosities of the epoxy resin compositions after being kept at 120° C. for 240 minutes were measured, and all of them were 180 mPa ⁇ s or less, and the impregnating properties into reinforcing fibers were particularly good.
- Example 21 had a wet heat 0° compressive strength of 1140 MPa and a post-impact compressive strength of 275 MPa, which were particularly favorable results.
- Example 23-26 An epoxy resin composition was prepared in the same manner as in Example 2, except that the binder species was changed. As a result of measuring the gelling temperature of the epoxy resin composition as described above, all of them were 175° C. or higher and 185° C. or lower, and the interfacial adhesion between the binder and the resin when the melting point of the binder was 165° C. or higher and 180° C. or lower. This was a particularly preferable temperature at which a uniform interlaminar thickness capable of sufficient plastic deformation in the fiber-reinforced composite material could be ensured. Next, the viscosities of the epoxy resin compositions after being kept at 120° C.
- cured resins were prepared by the method described above, and the Tg of the cured products was measured. Furthermore, a fiber-reinforced composite material was produced using this epoxy resin composition, and the 0° compressive strength under wet heat, the compressive strength after impact, and the number of microcracks were measured. The compressive strength after impact was 260 MPa or more, and the number of microcracks was less than 10, indicating good mechanical properties and durability.
- Example 21 has 5 or less microcracks
- Example 25 has a 0° compressive strength under wet heat of 1100 MPa and 5 or less microcracks
- Example 26 has 5 or less microcracks, which is particularly preferable. was the result.
- a resin cured product was prepared by the above-described method, and the Tg of the cured product was measured. In particular, heat resistance was good. Furthermore, a fiber-reinforced composite material was produced using this epoxy resin composition, and the 0° compressive strength under wet heat, the compressive strength after impact, and the number of microcracks were measured. Regarding the 0° compressive strength under wet heat, Comparative Example 1 was 990 MPa, which was lower than 1000 MPa, and the 0° compressive strength under wet heat was inferior, but Comparative Example 2 was 1270 MPa, which was a particularly favorable result.
- Comparative Example 1 was 285 MPa, which was a particularly favorable result, while Comparative Example 2 was 245 MPa, lower than 260 MPa, and inferior in impact resistance. Furthermore, the number of microcracks in Comparative Examples 1 and 2 was 5 or less, indicating particularly good durability.
- Example 4 An epoxy resin composition was prepared in the same manner as in Example 2, except that only component [C] was used as the curing agent and the content of each component was changed. As described above, the gelation temperature of the epoxy resin composition was measured and found to be 195°C, and the binder melted too much into the resin and the shape of the binder could not be maintained, so sufficient plastic deformation was possible in the fiber-reinforced composite material. It was a temperature at which a uniform interlayer thickness could not be ensured. Next, as a result of measuring the viscosity of the epoxy resin composition after holding it at 120° C. for 240 minutes, it was found to be 90 mPa ⁇ s, indicating that the impregnation of reinforcing fibers was particularly good.
- a resin cured product was prepared by the method described above, and the Tg of the cured product was measured. Furthermore, a fiber-reinforced composite material was produced using this epoxy resin composition, and the 0° compressive strength under wet heat, the compressive strength after impact, and the number of microcracks were measured. As a result, the compressive strength after impact was 255 MPa, which was lower than 260 MPa, the impact resistance was poor, and the number of microcracks was 5 or less, indicating particularly good durability.
- a resin cured product was produced by the method described above, and the Tg of the cured product was measured.
- Comparative Examples 5, 6, and 7 had a temperature of 175° C. or higher, which was a particularly favorable result.
- a fiber-reinforced composite material was produced using this epoxy resin composition, and the 0 ° compressive strength when wet heat, the compressive strength after impact, and the number of microcracks were measured.
- the compressive strength after impact was lower than 260 MPa, the number of microcracks was 10 or more, and the mechanical properties and durability were poor.
- a resin cured product was prepared by the method described above, and the Tg of the cured product was measured. Furthermore, a fiber-reinforced composite material was produced using this epoxy resin composition, and the 0 ° compressive strength when wet heat, the compressive strength after impact, and the number of microcracks were measured. The compressive strength after impact was lower than 260 MPa, the number of microcracks was 10 or more, and the mechanical properties and durability were poor.
- Example 7 except that instead of component [D] as a curing agent, a kind of curing agent other than component [C], component [D], and component [E] was used and the content ratio of each component was changed.
- An epoxy resin composition was prepared in the same manner. As a result of measuring the gelation temperature of the epoxy resin composition as described above, the binder that connects the reinforcing fiber base material begins to melt at a temperature higher than the gelation temperature of the epoxy resin composition, which is lower than 170 ° C. It was the temperature at which the interfacial adhesive strength decreased. Next, the viscosities of the epoxy resin compositions after being held at 120° C. for 240 minutes were measured.
- a resin cured product was prepared by the method described above, and the Tg of the cured product was measured. Furthermore, a fiber-reinforced composite material was produced using this epoxy resin composition, and the 0 ° compressive strength when wet heat, the compressive strength after impact, and the number of microcracks were measured. The compressive strength after impact was lower than 260 MPa, the number of microcracks was 10 or more, and the mechanical properties and durability were poor.
- the epoxy resin composition for a fiber-reinforced composite material of the present invention maintains a low resin viscosity for a long time during resin injection into a reinforcing fiber base material, so that it has good processability and a heating rate during heat curing. It is possible to impart high-level physical properties (heat resistance, high compressive strength, impact resistance, durability) to fiber-reinforced composite materials even for large structural materials such as aircraft wings, which may be slow to heat. As a result, the application of fiber-reinforced composite materials, especially for aircraft applications, will advance, and further weight reduction is expected to improve fuel efficiency and contribute to the reduction of greenhouse gas emissions.
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Abstract
Description
各実施例・比較例のエポキシ樹脂組成物を得るために、以下の樹脂原料を用いた。なお、表中のエポキシ樹脂組成物の欄における各成分の数値は含有量を示し、その単位は、特に断らない限り「質量部」である。
・“アラルダイト(登録商標)”MY721(N,N,N’,N’-テトラグリシジル-4,4’-ジアミノジフェニルメタン、エポキシ当量:113g/mol、ハンツマン・ジャパン(株)製)
2.[B]ビスフェノールF型エポキシ樹脂
・“EPICLON(登録商標)”830(ビスフェノールFのジグリシジルエーテル、エポキシ当量:170g/mol、DIC(株)製)
・“アラルダイト(登録商標)”GY282(ビスフェノールFのジグリシジルエーテル、エポキシ当量:171g/mol、ハンツマン・ジャパン(株)製)
3.成分[A]、成分[B]以外のエポキシ樹脂
・“EPICLON(登録商標)”850(ビスフェノールAのジグリシジルエーテル、エポキシ当量:188g/mol、DIC(株)製)。
4.[C]4,4’-メチレンビス(3-クロロ-2,6-ジエチルアニリン)
・“ロンザキュア(登録商標)”M-CDEA(4,4’-メチレンビス(3-クロロ-2,6-ジエチルアニリン、活性水素当量:95g/mol、ロンザ(株)製)。
5.[D]4,4’-メチレンビス(3,3’,5,5’-テトライソプロピルアニリン)
・“ロンザキュア(登録商標)”M-DIPA(4,4’-メチレンビス(3,3’,5,5’-テトライソプロピルアニリン)、活性水素当量:93g/mol、ロンザ(株)製)
6.[E]4,4’-メチレンビス(2-イソプロピル-6-メチルアニリン)
・“ロンザキュア(登録商標)”M-MIPA(3,3’-ジイソプロピル-5,5’-ジメチル-4,4’-ジアミノジフェニルメタン、活性水素当量:78g/mol、ロンザ(株)製)
7.成分[C]、成分[D]、成分[E]以外の硬化剤
・“ロンザキュア(登録商標)”M-DEA(3,3’,5,5’-テトラエチル-4,4’-ジアミノジフェニルメタン、活性水素当量:78g/mol、ロンザ(株)製)
・“カヤハード(登録商標)”A-A(PT)(2,2’-ジエチル-4,4’-ジアミノジフェニルメタンを主成分とする混合物、活性水素当量:64g/mol、液状、日本化薬(株)製)
8.添加剤
・“カネエース(登録商標)”MX-416(“アラルダイト(登録商標)”MY721:75質量%/コアシェルゴム粒子(体積平均粒子径:100nm、コア部分:架橋ポリブタジエン、シェル部分:メタクリル酸メチル/グリシジルメタクリレート/スチレン共重合ポリマー):25質量%のマスターバッチ、(株)カネカ製)
・“スタフィロイド(登録商標)”AC-3355(コアシェルゴム粒子(体積平均粒子径:500nm、コア部分:架橋ポリブチルアクリレート、シェル部分:架橋ポリスチレン、アイカ工業(株)製)。
表に記載した含有割合で各成分を混合し、エポキシ樹脂組成物を調製した。
上記で調製したエポキシ樹脂組成物を減圧下で脱泡した後、2mm厚の“テフロン(登録商標)”製スペーサーにより厚み2mmになるように設定したモールド中に注入した。180℃の温度で120分間硬化させ、厚さ2mmの樹脂硬化板を得た。
下記製造方法に従ってバインダーを作製した。
カプロラクタム1.2g、ラウロラクタム18.8g、イオン交換水10gを圧力容器に仕込んで密閉し、窒素置換した。加熱を開始して、缶内圧力が10kg/cm2に到達した後、水分を系外に放出させながら缶内圧力を10.0kg/cm2で保持し、内温170℃になると、50分かけて缶内圧力を常圧に戻し、更に窒素フロー下で2時間反応させ重合を完了した。その後、圧力容器からポリマーをガット状に吐出してペレタイズし、これを80℃で24時間真空乾燥して、ナイロン6/12(=6/94質量%)の共重合体PA-1を得た。1個のオリフィスを設けた口金から吐出したPA-1(融点:170℃)の繊維を、先端に衝撃板を設けたアスピレータと圧縮空気を用いて延伸した後、金網状に散布して捕集した。金網上に捕集した繊維シートを、加熱プレス機を用いて熱接着し、不織布形態のバインダー1を作製した。
1個のオリフィスを設けた口金から吐出したPES(住友化学(株)製“スミカエクセル(登録商標)”5003P、融点:なし)の繊維を、先端に衝撃板を設けたアスピレータと圧縮空気を用いて延伸した後、金網状に散布して捕集した。金網上に捕集した繊維シートを、加熱プレス機を用いて熱接着し、不織布形態のバインダー2を作製した。
1個のオリフィスを設けた口金から吐出したPA-2(東レ(株)製“アミラン(登録商標)”CM1001、融点:225℃)の繊維を、先端に衝撃板を設けたアスピレータと圧縮空気を用いて延伸した後、金網状に散布して捕集した。金網上に捕集した繊維シートを、加熱プレス機を用いて熱接着し、不織布形態のバインダー3を作製した。
1個のオリフィスを設けた口金から吐出したPA-3(アルケマ(株)製“Platamid(登録商標)”M1657、融点:110℃)の繊維を、先端に衝撃板を設けたアスピレータと圧縮空気を用いて延伸した後、金網状に散布して捕集した。金網上に捕集した繊維シートを、加熱プレス機を用いて熱接着し、不織布形態のバインダー4を作製した。
クレゾールノボラック型エポキシ樹脂(DIC(株)製“EPICLON(登録商標)”N-660)15質量部、ビスフェノール型エポキシ樹脂(三菱ケミカル(株)製“jER(登録商標)”825)25質量部、ポリエーテルスルホン(住友化学(株)製“スミカエクセル(登録商標)”PES5200P)60質量部を180℃の温度条件にて小型二軸押出機(S1KRCニーダー、(株)栗本鐵工所)を使用して混練を行ってバインダー樹脂組成物を調製した。調製したバインダー樹脂組成物をハンマーミル(PULVERIZER、ホソカワミクロン(株)製)にて、孔サイズ1mmのスクリーンを使用し、液体窒素を用いて凍結粉砕して粒子形態のバインダー5を得た。かかる粒子を目開きサイズ150μmと75μmの篩いに通し、目開きサイズ75μmの篩いに残ったバインダー粒子を評価に使用した。
得られたバインダーを、炭素繊維一方向織物(平織、縦糸:炭素繊維T800S-24K-10C 東レ(株)製、炭素繊維目付295g/m2、縦糸密度7.2本/25mm、横糸:ガラス繊維ECE225 1/0 1Z 日東紡(株)製、横糸密度7.5本/25mm)の片面に付着させた。付着量は、バインダー1からバインダー4の場合は5g/m2、バインダー5の場合は10g/m2とした。その後、遠赤外線ヒーターを使用して加熱し、バインダーを融着させ、片側表面にバインダーが付与されたバインダー付き強化繊維基材を得た。
各実施例における評価は以下の通りに行った。なお、測定n数は特に断らない限り、n=1である。
測定すべき検体を、熱硬化測定装置ATD-1000(Alpha Technologies(株)製)を用いて、70℃に加熱したステージにサンプルを投入し、昇温速度0.5℃/分で昇温しながら、周波数1.0Hz、歪み1%で動的粘弾性測定を行い、複素粘性率を求めた。このとき、複素粘性率が1.0×105Pa・sに達した温度をゲル化温度とした。なお、検体としては、各成分を混合し、1分間攪拌後のエポキシ樹脂組成物を用いた。
測定すべき検体を、JIS Z8803(1991)における「円すい-平板形回転粘度計による粘度測定方法」に従い、標準コーンローター(1°34’×R24)を装着したE型粘度計を使用して、120℃に保持した状態で測定した。E型粘度計としては、東京計器(株)製TVE-30Hを用いた。なお、検体としては、各成分を混合し、1分間攪拌後のエポキシ樹脂組成物を用いた。
樹脂硬化板から幅12.7mm、長さ40mmの試験片を切り出し、DMA装置ARES(TAインスツルメンツ社製)を用いてTg測定を行った。測定条件は、昇温速度5℃/分であった。測定で得られた貯蔵弾性率G’の変曲点での温度をTgとした。
400mm×400mm×1.2mmの板状キャビティを有する金型に、395mm×395mmに切り出した前記バインダー付き強化繊維基材を、繊維方向を0°として、0°方向に揃えて4枚積層したものをセットし、型締めを行った。続いて、金型を120℃に加熱した後、別途予め120℃に加熱したエポキシ樹脂組成物を、樹脂注入装置を用い、注入圧0.2MPaで成形型内に注入した。注入後、金型を120℃から180℃まで0.5℃/分で昇温して、180℃で2時間硬化した後、30℃まで降温して繊維強化複合材料を得た。
400mm×400mm×4.8mmの板状キャビティを有する金型に、395mm×395mmに切り出した前記バインダー付き強化繊維基材を、繊維方向を0°として、(45°/0°/-45°/90°)を3回繰り返して12枚積層した上に、(90°/-45°/0°/45°)を3回繰り返して12枚積層したものをセットして、型締めを行った。続いて、金型を120℃に加熱した後、予め別途120℃に加熱したエポキシ樹脂組成物を、樹脂注入装置を用い、注入圧0.2MPaで成形型内に注入した。注入後、金型を120℃から180℃まで0.5℃/分で昇温して、180℃で2時間硬化した後、30℃まで降温して繊維強化複合材料を得た。
上記(5)で得られた繊維強化複合材料から、幅75mm、長さ50mmの試験片を0°方向と長さ方向が同じになるようにしてカットした。得られた試験片を市販の恒温恒湿槽と環境試験機を用いて以下a、b、cの手順に示す環境条件にさらした。
表1-1に示すとおり、成分[A]として“アラルダイト(登録商標)”MY721を70質量部、成分[B]として“EPICLON(登録商標)”830を30質量部、成分[C]として“ロンザキュア(登録商標)”M-CDEAを59質量部、成分[D]として“ロンザキュア(登録商標)”M-DIPAを25質量部加え、80℃で1時間撹拌してエポキシ樹脂組成物を調製した。上記の通りに、エポキシ樹脂組成物のゲル化温度を測定した結果、177℃であり、バインダーと樹脂の界面接着性が良好かつバインダー形状を保つため、繊維強化複合材料において十分な塑性変形が可能な層間厚みを均一に確保できる特に好ましい温度であった。次に、120℃240分保持後のエポキシ樹脂組成物の粘度を測定した結果、140mPa・sであり、特に強化繊維への含浸性も良好であった。また、前述の方法により樹脂硬化物を作製し、硬化物のTgを測定した結果、175℃であり、特に耐熱性も良好であった。さらに、このエポキシ樹脂組成物を用いて繊維強化複合材料を作製し、湿熱時0°圧縮強度、衝撃後圧縮強度、マイクロクラック数を測定した結果、湿熱時0°圧縮強度が1060MPaと良好であり、衝撃後圧縮強度が280MPa、マイクロクラック数は5個以下と特に良好であった。
各成分の含有量を表1-1に示すように変更した以外は、実施例1と同様にエポキシ樹脂組成物を調製した。上記の通りに、エポキシ樹脂組成物のゲル化温度を測定した結果、いずれも170℃以上185℃以下であり、バインダーと樹脂の界面接着性が良好かつバインダー形状を保つため、繊維強化複合材料において十分な塑性変形が可能な層間厚みを均一に確保できる温度であった。その中でも、実施例2、3、5は175℃以上185℃以下であり、特に好ましい結果であった。次に、120℃240分保持後のエポキシ樹脂組成物の粘度を測定した結果、いずれも200mPa・s以下であり、強化繊維への含浸性も良好であった。その中でも、実施例2、3、5は180mPa・s以下であり、特に好ましい結果であった。また、前述の方法により樹脂硬化物を作製し、硬化物のTgを測定した結果、いずれも175℃以上であり、特に耐熱性も良好であった。さらに、このエポキシ樹脂組成物を用いて繊維強化複合材料を作製し、湿熱時0°圧縮強度、衝撃後圧縮強度、マイクロクラック数を測定した結果、いずれも湿熱時0°圧縮強度が1000MPa以上、衝撃後圧縮強度が260MPa以上、マイクロクラック数は10個未満と力学特性、耐久性も良好であった。その中でも、実施例2、3、5は湿熱時0°圧縮強度が1100MPa以上、衝撃後圧縮強度が270MPa以上、マイクロクラック数は5個以下であり、特に好ましい結果であった。
表1-1に示すとおり、成分[A]として“アラルダイト(登録商標)”MY721を80質量部、成分[B]として“EPICLON(登録商標)”830を20質量部、成分[C]として“ロンザキュア(登録商標)”M-CDEAを52質量部、成分[D]として“ロンザキュア(登録商標)”M-DIPAを17質量部、成分[E]として“ロンザキュア(登録商標)”M-MIPAを15質量部加え、80℃で1時間撹拌してエポキシ樹脂組成物を調製した。上記の通りに、エポキシ樹脂組成物のゲル化温度を測定した結果、170℃であり、バインダーと樹脂の界面接着性が良好かつバインダー形状を保つため、繊維強化複合材料において十分な塑性変形が可能な層間厚みを均一に確保できる温度であった。次に、120℃240分保持後のエポキシ樹脂組成物の粘度を測定した結果、200mPa・sであり、強化繊維への含浸性も良好であった。また、前述の方法により樹脂硬化物を作製し、硬化物のTgを測定した結果、186℃であり、特に耐熱性も良好であった。さらに、このエポキシ樹脂組成物を用いて繊維強化複合材料を作製し、湿熱時0°圧縮強度、衝撃後圧縮強度、マイクロクラック数を測定した結果、湿熱時0°圧縮強度が1030MPa、衝撃後圧縮強度が260MPa、マイクロクラック数は6個以上10個未満と良好であった。
各成分の含有量を表1-1、表1-2に示すように変更した以外は、実施例6と同様にエポキシ樹脂組成物を調製した。上記の通りに、エポキシ樹脂組成物のゲル化温度を測定した結果、いずれも175℃以上185℃以下であり、バインダーと樹脂の界面接着性が良好かつバインダー形状を保つため、繊維強化複合材料において十分な塑性変形が可能な層間厚みを均一に確保できる特に好ましい温度であった。次に、120℃240分保持後のエポキシ樹脂組成物の粘度を測定した結果、いずれも180mPa・s以下であり、特に強化繊維への含浸性も良好であった。また、前述の方法により樹脂硬化物を作製し、硬化物のTgを測定した結果、いずれも175℃以上であり、特に耐熱性も良好であった。さらに、このエポキシ樹脂組成物を用いて繊維強化複合材料を作製し、湿熱時0°圧縮強度、衝撃後圧縮強度、マイクロクラック数を測定した結果、いずれも湿熱時0°圧縮強度が1100MPa以上、衝撃後圧縮強度が270MPa以上、マイクロクラック数は5個以下と特に力学特性、耐久性も良好であった。
成分[B]として、“アラルダイト(登録商標)”GY282を使用した以外は、実施例7と同様にエポキシ樹脂組成物を調製した。上記の通りに、エポキシ樹脂組成物のゲル化温度を測定した結果、175℃であり、バインダーと樹脂の界面接着性が良好かつバインダー形状を保つため、繊維強化複合材料において十分な塑性変形が可能な層間厚みを均一に確保できる特に好ましい温度であった。次に、120℃240分保持後のエポキシ樹脂組成物の粘度を測定した結果、170mPa・sであり、特に強化繊維への含浸性も良好であった。また、前述の方法により樹脂硬化物を作製し、硬化物のTgを測定した結果、184℃であり、耐熱性も良好であった。さらに、このエポキシ樹脂組成物を用いて繊維強化複合材料を作製し、湿熱時0°圧縮強度、衝撃後圧縮強度、マイクロクラック数を測定した結果、湿熱時0°圧縮強度が1150MPaと良好であり、衝撃後圧縮強度が270MPa、マイクロクラック数は5個以下と特に良好であった。
成分[E]の代わりに、“ロンザキュア(登録商標)”M-DEAを使用した以外は、実施例7と同様にエポキシ樹脂組成物を調製した。上記の通りに、エポキシ樹脂組成物のゲル化温度を測定した結果、176℃であり、バインダーと樹脂の界面接着性が良好かつバインダー形状を保つため、繊維強化複合材料において十分な塑性変形が可能な層間厚みを均一に確保できる特に好ましい温度であった。次に、120℃240分保持後のエポキシ樹脂組成物の粘度を測定した結果、160mPa・sであり、特に強化繊維への含浸性も良好であった。また、前述の方法により樹脂硬化物を作製し、硬化物のTgを測定した結果、174℃であり、耐熱性も良好であった。さらに、このエポキシ樹脂組成物を用いて繊維強化複合材料を作製し、湿熱時0°圧縮強度、衝撃後圧縮強度、マイクロクラック数を測定した結果、湿熱時0°圧縮強度が1040MPaと良好であり、衝撃後圧縮強度が270MPa、マイクロクラック数は5個以下と特に良好であった。
各成分の含有量とH/Eを表1-2に示すように変更した以外は、実施例2と同様にエポキシ樹脂組成物を調製した。上記の通りに、エポキシ樹脂組成物のゲル化温度を測定した結果、いずれも170℃以上185℃以下であり、バインダーと樹脂の界面接着性が良好かつバインダー形状を保つため、繊維強化複合材料において十分な塑性変形が可能な層間厚みを均一に確保できる温度であった。その中でも、実施例11、12は175℃以上185℃以下であり、特に好ましい結果であった。次に、120℃240分保持後のエポキシ樹脂組成物の粘度を測定した結果、いずれも200mPa・s以下であり、強化繊維への含浸性も良好であった。その中でも、実施例11、12は180mPa・s以下であり、特に好ましい結果であった。また、前述の方法により樹脂硬化物を作製し、硬化物のTgを測定した結果、いずれも170℃以上であり、耐熱性も良好であった。その中でも、実施例11、12は175℃以上であり、特に好ましい結果であった。さらに、このエポキシ樹脂組成物を用いて繊維強化複合材料を作製し、湿熱時0°圧縮強度、衝撃後圧縮強度、マイクロクラック数を測定した結果、いずれも湿熱時0°圧縮強度が1000MPa以上、衝撃後圧縮強度が260MPa以上、マイクロクラック数は10個未満と力学特性、耐久性も良好であった。その中でも、実施例11はマイクロクラック数が5個以下であり、実施例12は湿熱時0°圧縮強度が1100MPa以上、衝撃後圧縮強度が270MPa以上、マイクロクラック数は5個以下であり、特に好ましい結果であった。
各成分の含有量及びH/Eを表1-2、表1-3に示すように変更した以外は、実施例7と同様にエポキシ樹脂組成物を調製した。上記の通りに、エポキシ樹脂組成物のゲル化温度を測定した結果、いずれも170℃以上185℃以下であり、バインダーと樹脂の界面接着性が良好かつバインダー形状を保つため、繊維強化複合材料において十分な塑性変形が可能な層間厚みを均一に確保できる温度であった。その中でも、実施例14、15は175℃以上185℃以下であり、特に好ましい結果であった。次に、120℃240分保持後のエポキシ樹脂組成物の粘度を測定した結果、いずれも200mPa・s以下であり、強化繊維への含浸性も良好であった。その中でも、実施例14、15は180mPa・s以下であり、特に好ましい結果であった。また、前述の方法により樹脂硬化物を作製し、硬化物のTgを測定した結果、いずれも170℃以上であり、耐熱性も良好であった。その中でも、実施例14、15は175℃以上であり、特に好ましい結果であった。さらに、このエポキシ樹脂組成物を用いて繊維強化複合材料を作製し、湿熱時0°圧縮強度、衝撃後圧縮強度、マイクロクラック数を測定した結果、いずれも湿熱時0°圧縮強度が1000MPa以上、衝撃後圧縮強度が260MPa以上、マイクロクラック数は10個未満と力学特性、耐久性も良好であった。その中でも、実施例14はマイクロクラック数が5個以下であり、実施例15は湿熱時0°圧縮強度が1140MPa、衝撃後圧縮強度が275MPa、マイクロクラック数は5個以下であり、特に好ましい結果であった。
表1-3に示すとおり、成分[A]として“アラルダイト(登録商標)”MY721を65質量部、成分[B]として“EPICLON(登録商標)”830を20質量部、成分[C]として“ロンザキュア(登録商標)”M-CDEAを61質量部、成分[D]として“ロンザキュア(登録商標)”M-DIPAを26質量部、成分[F]として“カネエース(登録商標)”MX-416を20質量部加え、80℃で1時間撹拌してエポキシ樹脂組成物を調製した。上記の通りに、エポキシ樹脂組成物のゲル化温度を測定した結果、177℃であり、バインダーと樹脂の界面接着性が良好かつバインダー形状を保つため、繊維強化複合材料において十分な塑性変形が可能な層間厚みを均一に確保できる特に好ましい温度であった。次に、120℃240分保持後のエポキシ樹脂組成物の粘度を測定した結果、170mPa・sであり、特に強化繊維への含浸性も良好であった。また、前述の方法により樹脂硬化物を作製し、硬化物のTgを測定した結果、182℃であり、特に耐熱性も良好であった。さらに、このエポキシ樹脂組成物を用いて繊維強化複合材料を作製し、湿熱時0°圧縮強度、衝撃後圧縮強度、マイクロクラック数を測定した結果、湿熱時0°圧縮強度が1100MPa、衝撃後圧縮強度が280MPa、マイクロクラック数は5個以下と特に力学特性、耐久性も良好であった。
各成分の含有量とコアシェルゴム粒子種を表1-3に示すように変更したこと以外は、実施例17と同様にエポキシ樹脂組成物を調製した。上記の通りに、エポキシ樹脂組成物のゲル化温度を測定した結果、いずれも175℃以上185℃以下であり、バインダーと樹脂の界面接着性が良好かつバインダー形状を保つため、繊維強化複合材料において十分な塑性変形が可能な層間厚みを均一に確保できる特に好ましい温度であった。次に、120℃240分保持後のエポキシ樹脂組成物の粘度を測定した結果、いずれも200mPa・s以下であり、強化繊維への含浸性も良好であった。その中でも、実施例19は170mPa・sであり、特に好ましい結果であった。また、前述の方法により樹脂硬化物を作製し、硬化物のTgを測定した結果、いずれも175℃以上であり、特に耐熱性も良好であった。さらに、このエポキシ樹脂組成物を用いて繊維強化複合材料を作製し、湿熱時0°圧縮強度、衝撃後圧縮強度、マイクロクラック数を測定した結果、いずれも湿熱時0°圧縮強度が1000MPa以上、衝撃後圧縮強度が260MPa以上と力学特性も良好で、マイクロクラック数は5個以下と特に耐久性も良好であった。その中でも、実施例18は衝撃後圧縮強度が280MPaであり、特に好ましい結果であった。
表1-3に示すとおり、成分[A]として“アラルダイト(登録商標)”MY721を65質量部、成分[B]として“EPICLON(登録商標)”830を20質量部、成分[C]として“ロンザキュア(登録商標)”M-CDEAを78質量部、成分[D]として“ロンザキュア(登録商標)”M-DIPAを5質量部、成分[E]として“ロンザキュア(登録商標)”M-MIPAを4質量部、成分[F]として“カネエース(登録商標)”MX-416を20質量部加え、80℃で1時間撹拌してエポキシ樹脂組成物を調製した。上記の通りに、エポキシ樹脂組成物のゲル化温度を測定した結果、184℃であり、バインダーと樹脂の界面接着性が良好かつバインダー形状を保つため、繊維強化複合材料において十分な塑性変形が可能な層間厚みを均一に確保できる特に好ましい温度であった。次に、120℃240分保持後のエポキシ樹脂組成物の粘度を測定した結果、120mPa・sであり、特に強化繊維への含浸性も良好であった。また、前述の方法により樹脂硬化物を作製し、硬化物のTgを測定した結果、180℃であり、特に耐熱性も良好であった。さらに、このエポキシ樹脂組成物を用いて繊維強化複合材料を作製し、湿熱時0°圧縮強度、衝撃後圧縮強度、マイクロクラック数を測定した結果、湿熱時0°圧縮強度が1120MPa、衝撃後圧縮強度が280MPa、マイクロクラック数は5個以下と特に力学特性、耐久性も良好であった。
各成分の含有量とコアシェルゴム粒子種を表1-4に示すように変更したこと以外は、実施例20と同様にエポキシ樹脂組成物を調製した。上記の通りに、エポキシ樹脂組成物のゲル化温度を測定した結果、いずれも175℃以上185℃以下であり、バインダーと樹脂の界面接着性が良好かつバインダー形状を保つため、繊維強化複合材料において十分な塑性変形が可能な層間厚みを均一に確保できる特に好ましい温度であった。次に、120℃240分保持後のエポキシ樹脂組成物の粘度を測定した結果、いずれも180mPa・s以下であり、特に強化繊維への含浸性も良好であった。また、前述の方法により樹脂硬化物を作製し、硬化物のTgを測定した結果、いずれも175℃以上であり、特に耐熱性も良好であった。さらに、このエポキシ樹脂組成物を用いて繊維強化複合材料を作製し、湿熱時0°圧縮強度、衝撃後圧縮強度、マイクロクラック数を測定した結果、いずれも湿熱時0°圧縮強度が1000MPa以上、衝撃後圧縮強度が260MPa以上と力学特性も良好で、マイクロクラック数は5個以下と特に耐久性も良好であった。その中でも、実施例21は湿熱時0°圧縮強度が1140MPa、衝撃後圧縮強度が275MPaであり、特に好ましい結果であった。
バインダー種を変更した以外は、実施例2と同様にエポキシ樹脂組成物を調製した。上記の通りに、エポキシ樹脂組成物のゲル化温度を測定した結果、いずれも175℃以上185℃以下であり、バインダーの融点が165℃以上180℃以下である際にバインダーと樹脂の界面接着性が良好かつバインダー形状を保つため、繊維強化複合材料において十分な塑性変形が可能な層間厚みを均一に確保できる特に好ましい温度であった。次に、120℃240分保持後のエポキシ樹脂組成物の粘度を測定した結果、いずれも180mPa・s以下であり、特に強化繊維への含浸性も良好であった。また、前述の方法により樹脂硬化物を作製し、硬化物のTgを測定した結果、いずれも175℃以上であり、特に耐熱性も良好であった。さらに、このエポキシ樹脂組成物を用いて繊維強化複合材料を作製し、湿熱時0°圧縮強度、衝撃後圧縮強度、マイクロクラック数を測定した結果、いずれも湿熱時0°圧縮強度が1000MPa以上、衝撃後圧縮強度が260MPa以上、マイクロクラック数は10個未満と力学特性、耐久性も良好であった。その中でも、実施例21はマイクロクラック数が5個以下、実施例25は湿熱時0°圧縮強度が1100MPa、マイクロクラック数が5個以下、実施例26はマイクロクラック数が5個以下と特に好ましい結果であった。
各成分の含有量を表2-1に示すように変更した以外は、実施例1と同様にエポキシ樹脂組成物を調製した。上記の通りに、エポキシ樹脂組成物のゲル化温度を測定した結果、いずれも175℃以上185℃以下であり、バインダーと樹脂の界面接着性が良好かつバインダー形状を保つため、繊維強化複合材料において十分な塑性変形が可能な層間厚みを均一に確保できる特に好ましい温度であった。次に、120℃240分保持後のエポキシ樹脂組成物の粘度を測定した結果、比較例1は100mPa・sと特に強化繊維への含浸性も良好であったが、比較例2は210mPa・sと、200mPa・sを超えており、強化繊維への含浸性が劣った。また、前述の方法により樹脂硬化物を作製し、硬化物のTgを測定した結果、比較例1は168℃と、170℃よりも低く、耐熱性に劣ったが、比較例2は196℃と特に耐熱性が良好であった。さらに、このエポキシ樹脂組成物を用いて繊維強化複合材料を作製し、湿熱時0°圧縮強度、衝撃後圧縮強度、マイクロクラック数を測定した。湿熱時0°圧縮強度について、比較例1は990MPaと、1000MPaよりも低く、湿熱時0°圧縮強度が劣ったが、比較例2は1270MPaと特に好ましい結果であった。次に、衝撃後圧縮強度について比較例1は285MPaと特に好ましい結果であったが、比較例2は245MPaと、260MPaよりも低く、耐衝撃性が劣った。さらに、マイクロクラック数について比較例1、2ともに5個以下と特に耐久性は良好であった。
成分[B]の代わりに、“EPICLON(登録商標)”850を使用したことと各成分の含有割合を変更したこと以外は、実施例2と同様にエポキシ樹脂組成物を調製した。上記の通りに、エポキシ樹脂組成物のゲル化温度を測定した結果、177℃であり、バインダーと樹脂の界面接着性が良好かつバインダー形状を保つため、繊維強化複合材料において十分な塑性変形が可能な層間厚みを均一に確保できる特に好ましい温度であった。次に、120℃240分保持後のエポキシ樹脂組成物の粘度を測定した結果、180mPa・sと特に強化繊維への含浸性も良好であった。また、前述の方法により樹脂硬化物を作製し、硬化物のTgを測定した結果、187℃と特に耐熱性が良好であった。さらに、このエポキシ樹脂組成物を用いて繊維強化複合材料を作製し、湿熱時0°圧縮強度、衝撃後圧縮強度、マイクロクラック数を測定した結果、湿熱時0°圧縮強度が980MPaと、1000MPaよりも低く、湿熱時0°圧縮強度が劣ったが、衝撃後圧縮強度は275MPaと特に耐衝撃性が良好であり、マイクロクラック数は5個以下と特に耐久性も良好であった。
硬化剤として成分[C]のみを使用したことと各成分の含有割合を変更したこと以外は、実施例2と同様にエポキシ樹脂組成物を調製した。上記の通りに、エポキシ樹脂組成物のゲル化温度を測定した結果、195℃であり、バインダーが樹脂に溶融し過ぎ、バインダー形状を保てないため、繊維強化複合材料において十分な塑性変形が可能な層間厚みを均一に確保できない温度であった。次に、120℃240分保持後のエポキシ樹脂組成物の粘度を測定した結果、90mPa・sと特に強化繊維への含浸性も良好であった。また、前述の方法により樹脂硬化物を作製し、硬化物のTgを測定した結果、178℃と特に耐熱性が良好であった。さらに、このエポキシ樹脂組成物を用いて繊維強化複合材料を作製し、湿熱時0°圧縮強度、衝撃後圧縮強度、マイクロクラック数を測定した結果、湿熱時0°圧縮強度が1100MPaと特に良好な結果であり、衝撃後圧縮強度は255MPaと、260MPaよりも低く、耐衝撃性が劣り、マイクロクラック数は5個以下と特に耐久性が良好であった。
硬化剤として成分[D]または成分[E]または成分[C]・成分[D]・成分[E]以外の硬化剤一種のみを使用したことと各成分の含有割合を変更したこと以外は、比較例4と同様にエポキシ樹脂組成物を調製した。上記の通りに、エポキシ樹脂組成物のゲル化温度を測定した結果、いずれも170℃より低く、エポキシ樹脂組成物のゲル化温度より高い温度で強化繊維基材を連結するバインダーが融解しだすため、界面接着強度が低下する温度であった。次に、120℃240分保持後のエポキシ樹脂組成物の粘度を測定した結果、いずれも1000mPa・sより大きく、200mPa・sを超えており、強化繊維への含浸性が劣った。また、前述の方法により樹脂硬化物を作製し、硬化物のTgを測定した結果、170℃以上であり、耐熱性は良好であった。その中でも、比較例5、6、7は175℃以上であり、特に好ましい結果であった。さらに、このエポキシ樹脂組成物を用いて繊維強化複合材料を作製し、湿熱時0°圧縮強度、衝撃後圧縮強度、マイクロクラック数を測定した結果、いずれも湿熱時0°圧縮強度が1000MPaよりも低く、衝撃後圧縮強度が260MPaよりも低く、マイクロクラック数は10個以上と力学特性、耐久性が不良であった。
硬化剤として成分[D]の代わりに、成分[E]または成分[C]・成分[D]・成分[E]以外の硬化剤一種を使用したことと各成分の含有割合を変更したこと以外は、実施例2と同様にエポキシ樹脂組成物を調製した。上記の通りに、エポキシ樹脂組成物のゲル化温度を測定した結果、いずれも170℃より低く、エポキシ樹脂組成物のゲル化温度より高い温度で強化繊維基材を連結するバインダーが融解しだすため、界面接着強度が低下する温度であった。次に、120℃240分保持後のエポキシ樹脂組成物の粘度を測定した結果、いずれも200mPa・sを超えており、強化繊維への含浸性が劣った。また、前述の方法により樹脂硬化物を作製し、硬化物のTgを測定した結果、175℃以上であり、耐熱性は特に良好であった。さらに、このエポキシ樹脂組成物を用いて繊維強化複合材料を作製し、湿熱時0°圧縮強度、衝撃後圧縮強度、マイクロクラック数を測定した結果、いずれも湿熱時0°圧縮強度が1000MPaよりも低く、衝撃後圧縮強度が260MPaよりも低く、マイクロクラック数は10個以上と力学特性、耐久性が不良であった。
硬化剤として成分[D]の代わりに、成分[C]・成分[D]・成分[E]以外の硬化剤一種を使用したことと各成分の含有割合を変更したこと以外は、実施例7と同様にエポキシ樹脂組成物を調製した。上記の通りに、エポキシ樹脂組成物のゲル化温度を測定した結果、いずれも170℃より低く、エポキシ樹脂組成物のゲル化温度より高い温度で強化繊維基材を連結するバインダーが融解しだすため、界面接着強度が低下する温度であった。次に、120℃240分保持後のエポキシ樹脂組成物の粘度を測定した結果、いずれも200mPa・sを超えており、強化繊維への含浸性が劣った。また、前述の方法により樹脂硬化物を作製し、硬化物のTgを測定した結果、175℃以上であり、耐熱性は特に良好であった。さらに、このエポキシ樹脂組成物を用いて繊維強化複合材料を作製し、湿熱時0°圧縮強度、衝撃後圧縮強度、マイクロクラック数を測定した結果、いずれも湿熱時0°圧縮強度が1000MPaよりも低く、衝撃後圧縮強度が260MPaよりも低く、マイクロクラック数は10個以上と力学特性、耐久性が不良であった。
Claims (11)
- [A]テトラグリシジルジアミノジフェニルメタンを、全エポキシ樹脂成分100質量%中に70質量%以上90質量%以下含み、かつ[B]ビスフェノールF型エポキシ樹脂を、全エポキシ樹脂成分100質量%中に10質量%以上30質量%以下含み、かつ[C]4,4’-メチレンビス(3-クロロ-2,6-ジエチルアニリン)及び[D]4,4’-メチレンビス(3,3’,5,5’-テトライソプロピルアニリン)を含む繊維強化複合材料用エポキシ樹脂組成物。
- さらに[E]4,4’-メチレンビス(2-イソプロピル-6-メチルアニリン)を含む請求項1に記載の繊維強化複合材料用エポキシ樹脂組成物。
- さらに[F]体積平均粒子径が50nm以上300nm以下の範囲内にある、シェル部分にエポキシ基を含むコアシェルゴム粒子を含む請求項1または2に記載の繊維強化複合材料用エポキシ樹脂組成物。
- E型粘度計による等温測定より得られる、120℃一定で240分後の樹脂粘度η(mPa・s)が20≦η≦200を満たす請求項1から3のいずれかに記載の繊維強化複合材料用エポキシ樹脂組成物。
- 70℃から昇温速度0.5℃/分で加熱した際のゲル化温度が170℃以上185℃以下の範囲内にある、請求項1から4のいずれかに記載の繊維強化複合材料用エポキシ樹脂組成物。
- 請求項1から5のいずれかに記載の繊維強化複合材料用エポキシ樹脂組成物の硬化物と、強化繊維基材とを含む繊維強化複合材料。
- 前記強化繊維基材が不織布形態のバインダーで連結されたプリフォームである、請求項6に記載の繊維強化複合材料。
- 前記不織布形態のバインダーが、融点165℃以上180℃以下のポリアミドからなる請求項7に記載の繊維強化複合材料。
- 繊維強化基材の表面に付着した前記不織布形態のバインダーの付着量が、片面当たり0.5g/m2以上10g/m2以下である請求項7または8に記載の繊維強化複合材料。
- 前記繊維強化基材を構成する強化繊維が炭素繊維である、請求項6から9のいずれかに記載の繊維強化複合材料。
- 50℃以上130℃以下に加熱した請求項1から5のいずれかに記載の繊維強化複合材料用エポキシ樹脂組成物を、90℃以上180℃以下に加熱した成形型内に配置した強化繊維基材に注入し、含浸させ、該成形型内で硬化する繊維強化複合材料の製造方法。
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