Patent Application
20160280872
The present invention relates to a prepreg, a fiber-reinforced composite material, and a resin composition containing particles used for the preparation of them. The present invention particularly relates to a fiber-reinforced composite material for aircraft uses, vessel uses, automobile uses, sports uses, and other general industrial uses and a prepreg used to obtain the composite material.
Fiber-reinforced composite materials made of various fibers and matrix resins are widely used for aircraft, vessels, automobiles, sports equipment, other general industrial uses, etc. because of their excellent mechanical properties. In recent years, with actual uses of them, the range of use of fiber-reinforced composite materials has been becoming wider and wider.
As such fiber-reinforced composite materials, ones using a benzoxazine resin are proposed in, for example, Patent Literatures 1 and 2. The benzoxazine resin has excellent moisture resistance and heat resistance, but has the problem of being inferior in toughness; and measures in which epoxy resins, various resin fine particles, etc. are blended to make up for the disadvantage are taken.
Patent Literature 1: Japanese Unexamined Patent Publication No. 2007-16121
Patent Literature 2: Japanese Unexamined Patent Publication No. 2010-13636
For fiber-reinforced composite materials for aircraft uses, further weight reduction is desired. To reduce the weight of the material, it is necessary to achieve, in particular, a compressive strength after impact (hereinafter, abbreviated as a CAI) and a flexural modulus out of the mechanical characteristics needed for aircraft uses at high level at the same time, and it is also necessary for the glass transition temperature of the resin material used to be kept high in order to maintain high temperature characteristics. Further, it is also one of important characteristics of a fiber-reinforced composite material, which is typically formed by stacking a prepreg plurally and heating the prepregs, that peeling between the fiber layers is less likely to occur. However, it cannot necessarily be said that these can be achieved at high level at the same time in the examples specifically described in Patent Literatures above.
An object of the present invention is to provide a prepreg that makes it possible to obtain a fiber-reinforced composite material that, while using a benzoxazine resin having excellent moisture resistance and heat resistance, can achieve interlaminar fracture toughness, CAI and flexural modulus at high level at the same time and can also keep the glass transition temperature of the resin material high, a resin composition containing particles for obtaining the prepreg, and a fiber-reinforced composite material.
To solve the problem mentioned above, the present invention provides a prepreg comprising: a reinforcing fiber layer including reinforcing fibers and a resin composition with which the space between fibers of the reinforcing fibers is impregnated and which contains (A) a benzoxazine resin, (B) an epoxy resin, and (C) a curing agent having 2 or more phenolic hydroxy groups in a molecule; and a surface layer provided on at least one surface of the reinforcing fiber layer and containing (A) a benzoxazine resin, (B) an epoxy resin, (C) a curing agent having 2 or more phenolic hydroxy groups in a molecule, and (D) polyamide resin particles having an average particle size of 5 to 50 μm, wherein the polyamide resin particles include a polyamide 12 resin particle and a polyamide resin particle made of a copolymer in which caprolactam and laurolactam are copolymerized at a molar ratio of 9:1 to 7:3.
By the prepreg of the present invention being stacked plurally and heated under increased pressure, a fiber-reinforced composite material that, while using a benzoxazine resin having excellent moisture resistance and heat resistance, can achieve interlaminar fracture toughness, CAI and flexural modulus at high level at the same time and can also keep the glass transition temperature of the resin material high can be obtained.
The present inventors presume the reason why the interlaminar fracture toughness, CAI and flexural modulus can be improved by the prepreg mentioned above as follows. A decrease in the melting temperature of the polyamide resin particles occurs due to the presence of the compound having phenolic hydroxy groups that is the curing agent of the benzoxazine resin. Here, if the melting temperature of the polyamide resin particles is too low, during the curing of the thermosetting resin in preparing a fiber-reinforced composite material using the prepreg, the polyamide resin particles are likely to melt and the melted polyamide resin particles are likely to enter the reinforcing fiber layer. The reason is considered that, by using two types of the specific polyamide resin particles mentioned above, one polyamide resin particle can be melted moderately while the other polyamide resin particle is kept in a state where it is difficult for the polyamide resin particle to flow under temperature conditions for sufficiently curing the (A) to (C) components mentioned above, and as a result a resin cured layer excellent in adhesiveness, peel resistance, and flexural modulus has been formed between the fiber layers.
According to research by the present inventors, it has been revealed that a prepreg obtained by using one type of polyamide resin particles may have influence on evaluation results of CAI, mode I interlaminar fracture toughness (G1c), mode II interlaminar fracture toughness (G2c), or the like depending on temperature increase conditions in heating a stacked body thereof By the prepreg of the present invention, such variation in physical properties due to the difference in heating conditions can be suppressed, and interlaminar fracture toughness and CAI at high level can be obtained stably.
It is preferable that the surface layer mentioned above contain 65 to 78 parts by mass of the (A) component mentioned above, 22 to 35 parts by mass of the (B) component mentioned above, 5 to 20 parts by mass of the (C) component mentioned above, and 15 to 45 parts by mass of the (D) component mentioned above when it is assumed that the total amount of the (A) component mentioned above and the (B) component mentioned above is 100 parts by mass. By setting the amount of each of the components contained in the surface layer in the range mentioned above, each melting temperature of the polyamide 12 resin particles and the polyamide resin particles made of a copolymer in which caprolactam and laurolactam are copolymerized at a molar ratio of 9:1 to 7:3 in the surface layer can be in a moderate range; a moderate melting can be generated while sufficiently suppressing the polyamide 12 resin particle entering the reinforcing fiber layer; and the interlaminar fracture toughness, CAI, and flexural modulus can be more improved.
The present invention also provides a fiber-reinforced composite material obtained by stacking the prepreg according to the present invention mentioned above plurally and performing heating under increased pressure.
By being obtained from the prepreg according to the present invention, the fiber-reinforced composite material of the present invention has excellent moisture resistance and heat resistance and can achieve interlaminar fracture toughness, CAI and flexural modulus at high level at the same time. By the fiber-reinforced composite material of the present invention, the weight of the material can be reduced through the excellent physical properties mentioned above.
The present invention also provides a resin composition containing particles comprising (A) a benzoxazine resin, (B) an epoxy resin, (C) a curing agent having 2 or more phenolic hydroxy groups in a molecule, and (D) polyamide resin particles having an average particle size of 5 to 50 μm, wherein the polyamide resin particles include a polyamide 12 resin particle and a polyamide resin particle made of a copolymer in which caprolactam and laurolactam are copolymerized at a molar ratio of 9:1 to 7:3.
By the resin composition containing particles of the present invention, the surface layer of the prepreg according to the present invention described above can be prepared.
According to the present invention, a prepreg that makes it possible to obtain a fiber-reinforced composite material that, while using a benzoxazine resin having excellent moisture resistance and heat resistance, can achieve interlaminar fracture toughness, CAI and flexural modulus at high level at the same time and can also keep the glass transition temperature of the resin material high, a resin composition containing particles for obtaining the prepreg, and a fiber-reinforced composite material can be provided.
The fiber-reinforced composite material of the present invention can be suitably used for aircraft uses, vessel uses, automobile uses, sports uses, and other general industrial uses, and is useful particularly for aircraft uses.
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Suitable embodiments of the present invention will now be described in detail.
In the prepregs 10 and 12 according to the embodiment, the resin composition 2 contains (A) a benzoxazine resin, (B) an epoxy resin, and (C) a curing agent having 2 or more phenolic hydroxy groups in a molecule; the surface layers 6a and 6b contain (A) a benzoxazine resin, (B) an epoxy resin, (C) a curing agent having 2 or more phenolic hydroxy groups in a molecule, and (D) polyamide resin particles having an average particle size of 5 to 50 μm; and the polyamide resin particles include a polyamide 12 resin particle and a polyamide resin particle made of a copolymer in which caprolactam and laurolactam are copolymerized at a molar ratio of 9:1 to 7:3.
As (A) the benzoxazine resin used in the embodiment (hereinafter, occasionally referred to as an (A) component), a compound having a benzoxazine ring represented by the following formula (A-1) is given.
In formula (A-1), R5 represents a linear alkyl group having 1 to 12 carbon atoms, a cyclic alkyl group having 3 to 8 carbon atoms, an aryl group having 6 to 14 carbon atoms, or an aryl group substituted with a linear alkyl group having 1 to 12 carbon atoms or a halogen. A hydrogen atom may be bonded to the bond.
Examples of the linear alkyl group having 1 to 12 carbon atoms include a methyl group, an ethyl group, a propyl group, an isopropyl group, a n-butyl group, an isobutyl group, and a t-butyl group. Examples of the cyclic alkyl group having 3 to 8 carbon atoms include a cyclopentyl group and a cyclohexyl group. Examples of the aryl group having 6 to 14 carbon atoms include a phenyl group, a 1-naphthyl group, a 2-naphthyl group, a phenanthryl group, and a biphenyl group. Examples of the aryl group substituted with a linear alkyl group having 1 to 12 carbon atoms or a halogen include an o-tolyl group, a m-tolyl group, a p-tolyl group, a xylyl group, an o-ethylphenyl group, a m-ethylphenyl group, a p-ethylphenyl group, an o-t-butylphenyl group, a m-t-butylphenyl group, a p-t-butylphenyl group, an o-chlorophenyl group, and an o-bromophenyl group.
As R5, of the examples mentioned above, a methyl group, an ethyl group, a propyl group, a phenyl group, and an o-methylphenyl group are preferable because of providing good handleability.
Furthermore, as (A) the benzoxazine resin, a compound having benzoxazine rings represented by the following formula (A-2) is given.
In formula (A-2), L represents an alkylene group or an arylene group.
Preferred examples of the benzoxazine resin of the (A) component include the monomers represented by the following formulae, oligomers in which several molecules of the monomers are polymerized, and reaction products of at least one of the monomers represented by the following formulae and a compound having a benzoxazine ring having a structure different from these monomers.
The (A) component forms a skeleton similar to phenol resins by the benzoxazine ring polymerizing by ring-opening, and is therefore excellent in fire retardancy. Furthermore, excellent mechanical characteristics such as a low percentage of water absorption and a high elastic modulus are obtained because of its dense structure.
The (A) component may be used singly or in combinations of two or more.
(B) the epoxy resin (hereinafter, occasionally referred to as a (B) component) used in the embodiment controls the viscosity of the composition, and is blended as a component that enhances the curability of the composition. Preferred examples of the (B) component include epoxy resins produced using a compound such as amines, phenols, carboxylic acids, and compounds having a carbon-carbon double bond as a precursor.
Examples of the epoxy resins produced using amines as a precursor include tetraglycidyldiaminodiphenylmethane, glycidyl compounds of xylenediamine, triglycidylaminophenol, and glycidylaniline, and regioisomers of each thereof and alkyl group- or halogen-substituted products thereof. Hereinafter, when commercially available products are given as examples, for liquid products, the complex viscoelastic modulus η at 25° C. obtained with a dynamic viscoelasticity measurement apparatus described later is written as the viscosity.
Examples of the commercially available products of tetraglycidyldiaminodiphenylmethane include “SUMI-EPDXY” (registered trademark, the same applies hereinafter) ELM 434 (manufactured by Sumitomo Chemical Company, Limited), “Araldite” (registered trademark, the same applies hereinafter) MY 720, “Araldite” MY 721, “Araldite” MY 9512, “Araldite” MY 9612, “Araldite” MY 9634, and “Araldite” MY 9663 (all manufactured by Huntsman Advanced Materials), and “jER” (registered trademark, the same applies hereinafter) 604 (manufactured by Mitsubishi Chemical Corporation).
Examples of the commercially available products of triglycidylaminophenol include “jER” 630 (viscosity: 750 mPa·s) (manufactured by Mitsubishi Chemical Corporation), “Araldite” MY 0500 (viscosity: 3500 mPa·s) and MY 0510 (viscosity: 600 mPa·s) (both manufactured by Huntsman Advanced Materials), and ELM 100 (viscosity: 16000 mPa·s) (manufactured by Sumitomo Chemical Company, Limited).
Examples of the commercially available products of glycidylanilines include GAN (viscosity: 120 mPa·s) and GOT (viscosity: 60 mPa·s) (both manufactured by Nippon Kayaku Co., Ltd.).
Examples of the glycidyl ether-type epoxy resins produced using phenols as a precursor include bisphenol A-type epoxy resins, bisphenol F-type epoxy resins, bisphenol S-type epoxy resins, epoxy resins having a biphenyl skeleton, phenol novolac-type epoxy resins, cresol novolac-type epoxy resins, resorcinol-type epoxy resins, epoxy resins having a naphthalene skeleton, trisphenylmethane-type epoxy resins, phenolaralkyl-type epoxy resins, dicyclopentadiene-type epoxy resins, and diphenylfluorene-type epoxy resins, and various isomers of each thereof and alkyl group- or halogen-substituted products thereof. Also epoxy resins obtained by modifying epoxy resins produced using phenols as a precursor with a urethane or an isocyanate are included in this type.
Examples of the commercially available products of liquid bisphenol A-type epoxy resins include “jER” 825 (viscosity: 5000 mPa·s), “jER” 826 (viscosity: 8000 mPa·s), “jER” 827 (viscosity: 10000 mPa·s), and “jER” 828 (viscosity: 13000 mPa·s) (all manufactured by Mitsubishi Chemical Corporation), “EPICLON” (registered trademark, the same applies hereinafter) 850 (viscosity: 13000 mPa·s) (manufactured by DIC Corporation), “Epotohto” (registered trademark, the same applies hereinafter) YD-128 (viscosity: 13000 mPa·s) (manufactured by Nippon Steel Chemical Co., Ltd.), and DER-331 (viscosity: 13000 mPa·s) and DER-332 (viscosity: 5000 mPa·s) (manufactured by The Dow Chemical Company). Examples of the commercially available products of solid or semisolid bisphenol A-type epoxy resins include “jER” 834, “jER” 1001, “jER” 1002, “jER” 1003, “jER” 1004, “jER” 1004AF, “jER” 1007, and “jER” 1009 (all manufactured by Mitsubishi Chemical Corporation).
Examples of the commercially available products of liquid bisphenol F-type epoxy resins include “jER” 806 (viscosity: 2000 mPa·s), “jER” 807 (viscosity: 3500 mPa·s), and “jER” 1750 (viscosity: 1300 mPa·s) (all manufactured by Mitsubishi Chemical Corporation), “EPICLON” 830 (viscosity: 3500 mPa·s) (manufactured by DIC Corporation), and “Epotohto” YD-170 (viscosity: 3500 mPa·s) and “Epotohto” YD-175 (viscosity: 3500 mPa·s) (both manufactured by Nippon Steel Chemical Co., Ltd.). Examples of the commercially available products of solid bisphenol F-type epoxy resins include 4004P, “jER” 4007P, and “jER” 4009P (all manufactured by Mitsubishi Chemical Corporation) and “Epotohto” YDF 2001 and “Epotohto” YDF 2004 (both manufactured by Nippon Steel Chemical Co., Ltd.).
Examples of the commercially available products of bisphenol S-type epoxy resins include EXA-1515 (manufactured by DIC Corporation).
Examples of the commercially available products of epoxy resins having a biphenyl skeleton include “jER” YX4000H, “jER” YX4000, and “jER” YL6616 (all manufactured by Mitsubishi Chemical Corporation) and NC-3000 (manufactured by Nippon Kayaku Co., Ltd.).
Examples of the commercially available products of phenol novolac-type epoxy resins include “jER” 152 and “jER” 154 (both manufactured by Mitsubishi Chemical Corporation) and “EPICLON” N-740, “EPICLON” N-770, and “EPICLON” N-775 (all manufactured by DIC Corporation).
Examples of the commercially available products of cresol novolac-type epoxy resins include “EPICLON” N-660, “EPICLON” N-665, “EPICLON” N-670, “EPICLON” N-673, and “EPICLON” N-695 (all manufactured by DIC Corporation) and EOCN-1020, EOCN-102S, and EOCN-104S (all manufactured by Nippon Kayaku Co., Ltd.).
Examples of the commercially available products of resorcinol-type epoxy resins include “Denacol” (registered trademark, the same applies hereinafter) EX-201 (viscosity: 250 mPa·s) (manufactured by Nagase ChemteX Corporation).
Examples of the commercially available products of epoxy resins having a naphthalene skeleton include “EPICLON” HP 4032 (manufactured by DIC Corporation) and NC-7000 and NC-7300 (both manufactured by Nippon Kayaku Co., Ltd.).
Examples of the commercially available products of trisphenylmethane-type epoxy resins include TMH-574 (manufactured by Sumitomo Chemical Company, Limited).
Examples of the commercially available products of dicyclopentadiene-type epoxy resins include “EPICLON” HP 7200, “EPICLON” HP 7200L, and “EPICLON” HP 7200H (all manufactured by DIC Corporation), “Tactix” (registered trademark) 558 (manufactured by Huntsman Advanced Materials), and XD-1000-1L and XD-1000-2L (both manufactured by Nippon Kayaku Co., Ltd.).
Examples of the commercially available products of urethane and isocyanate-modified epoxy resins include AER 4152 having an oxazolidone ring (manufactured by Asahi Kasei E-materials Corporation).
Examples of the epoxy resins produced using a carboxylic acid as a precursor include glycidyl compounds of phthalic acid, glycidyl compounds of hexahydrophthalic acid and glycidyl compounds of dimer acids, and various isomers of each of them.
Examples of the commercially available products of phthalic acid diglycidyl esters include “EPOMIK” (registered trademark, the same applies hereinafter) R508 (viscosity: 4000 mPa·s) (manufactured by Mitsui Chemicals, Inc.) and “Denacol” EX-721 (viscosity: 980 mPa·s) (manufactured by Nagase ChemteX Corporation).
Examples of the commercially available products of hexahydrophthalic acid diglycidyl esters include “EPOMIK” R540 (viscosity: 350 mPa·s) (manufactured by Mitsui Chemicals, Inc.) and AK-601 (viscosity: 300 mPa·s) (manufactured by Nippon Kayaku Co., Ltd.).
Examples of the commercially available products of dimer acid diglycidyl esters include “jER” 871 (viscosity: 650 mPa·s) (manufactured by Mitsubishi Chemical Corporation) and “Epotohto” YD-171 (viscosity: 650 mPa·s) (manufactured by Nippon Steel Chemical Co., Ltd.).
Examples of the epoxy resins produced using compounds having a carbon-carbon double bond as a precursor include alicyclic epoxy resins. Examples of the alicyclic epoxy resins include (3′,4′-epoxycyclohexane)methyl-3,4-epoxycyclohexanecarboxylate, (3′,4′-epoxycyclohexane)octyl-3,4-epoxycyclohexanecarboxylate, and 1-methyl-4-(2-methyloxiranyl)-7-oxabicyclo[4.1.0]heptane.
Examples of the commercially available products of (3′,4′-epoxycyclohexane)methyl-3,4-epoxycyclohexanecarboxylate include “CELLOXIDE” (registered trademark, the same applies hereinafter) 2021P (viscosity: 250 mPa·s) (manufactured by Daicel
Chemical Industries, Ltd.) and CY 179 (viscosity: 400 mPa·s) (manufactured by Huntsman Advanced Materials); examples of the commercially available products of (3′,4′-epoxycyclohexane)octyl-3,4-epoxycyclohexanecarboxylate include “CELLOXIDE” 2081 (viscosity: 100 mPa·s) (manufactured by Daicel Chemical Industries, Ltd.); and examples of the commercially available products of 1-methyl-4-(2-methyloxiranyl)-7-oxabicyclo[4.1.0]heptane include “CELLOXIDE” 3000 (viscosity: 20 mPa·s) (manufactured by Daicel Chemical Industries, Ltd.).
In the embodiment, an epoxy resin that is in a liquid form at 25° C. may be blended from the viewpoints of tackiness and draping properties. It is preferable that the viscosity at 25° C. of the epoxy resin that is in a liquid form at 25° C. be as low as possible from the viewpoints of tackiness and draping properties. Specifically, 5 mPa·s or more, which is the lower limit obtained with commercially available products of epoxy resins, and 20000 mPa·s or less are preferable, and 5 mPa·s or more and 15000 mPa·s or less are more preferable. If the viscosity at 25° C. is more than 20000 mPa·s, tackiness or draping properties may be reduced.
On the other hand, an epoxy resin that is in a solid form at 25° C. may be blended from the viewpoint of heat resistance. As the epoxy resin that is in a solid form at 25° C., epoxy resins having a high aromatic content are preferable; and examples include epoxy resins having a biphenyl skeleton, epoxy resins having a naphthalene skeleton, and phenolaralkyl-type epoxy resins.
The (B) component may be used singly or in combinations of two or more.
As (C) the curing agent having 2 or more phenolic hydroxy groups in a molecule (hereinafter, occasionally referred to as a (C) component) used in the embodiment, polyfunctional phenols such as bisphenols are given; and examples include bisphenol A, bisphenol F, bisphenol S, thiodiphenol, and bisphenols represented by the following formula (C-1).
In formula (C-1), R1, R2, R3, and R4 represent a hydrogen atom or a hydrocarbon group; when R1, R2, R3, or R4 is a hydrocarbon group, they are a linear or branched alkyl group having 1 to 4 carbon atoms, or adjacent R1 and R2 or adjacent R3 and R4 bind to form a substituted or unsubstituted aromatic ring having 6 to 10 carbon atoms or a substituted or unsubstituted alicyclic structure having 6 to 10 carbon atoms; and x represents 0 or 1.
Examples of the curing agent represented by the above formula (C-1) include the compounds represented by the following formulae.
In the embodiment, from the viewpoint of sufficiently increasing the glass transition temperature of the resin cured substance, bisphenol A, bisphenol F, thiobisphenol (hereinafter, occasionally referred to as TDP), 9,9-bis(4-hydroxyphenyl)fluorene (hereinafter, occasionally referred to as BPF), and 1,1-bis(4-hydroxyphenyl)cyclohexane (hereinafter, occasionally referred to as BPC) are preferable.
The (C) component may be used singly or in combinations of two or more.
In the embodiment, a curing agent other than the (C) component mentioned above may be used in combination. Examples of the curing agent that can be used in combination include tertiary aromatic amines typified by N,N-dimethylaniline, tertiary aliphatic amines such as triethylamine, imidazole derivatives, and pyridine derivatives. These may be used singly or in combinations of two or more.
(D) the polyamide resin particles having an average particle size of 5 to 50 μm (hereinafter, occasionally referred to as a (D) component) used in the embodiment include (D1) a polyamide 12 resin particle (hereinafter, occasionally referred to as a (D1) component) and (D2) a polyamide resin particle made of a copolymer in which caprolactam and laurolactam are copolymerized at a molar ratio of 9:1 to 7:3 (hereinafter, occasionally referred to as a (D2) component). Here, the average particle size refers to the average value of the measured lengths of the major axes of 100 particles selected arbitrarily from particles that are magnified 200 to 500 times with a scanning electron microscope (SEM).
In the present specification, the polyamide 12 resin refers to a polyamide resin in which laurolactam is polymerized by ring-opening.
As the polyamide 12 resin particles used in the embodiment, commercially available products may be used; examples include “VESTOSINT 1111”, “VESTOSINT 2070”, “VESTOSINT 2157”,
“VESTOSINT 2158”, and “VESTOSINT 2159” (registered trade mark, all manufactured by Daicel-Evonik Ltd.); and “Orgasol 2002 D”, “Orgasol 2002 EXD”, and “Orgasol 2002 ES3” (registered trade mark, all manufactured by ARKEMA K.K.). It is preferable that the polyamide 12 resin particles be spherical particles, from the viewpoint of preventing the flow characteristics of the resin composition in which the particles are blended from being lowered, but may be non-spherical particles.
As the average particle size of the polyamide 12 resin particles, 5 to 50 μm are preferable and 10 to 30 μm are more preferable from the viewpoint of controlling the thickness of the surface layer.
The copolymer mentioned above in which caprolactam and laurolactam are copolymerized at a molar ratio of 9:1 to 7:3 is what is called polyamide 6/12 or the like. The copolymer mentioned above may be a random copolymer, or may be a block copolymer.
In the copolymer mentioned above, for the copolymerization ratio (molar ratio) of caprolactam and laurolactam, it is necessary to be in the range of 9:1 to 7:3, it is preferable to be in the range of 9:1 to 75:25, and it is more preferable to be in the range of 9:1 to 8:2. By setting the copolymerization ratio in the range mentioned above, the melting point of the polyamide resin particles and the melting temperature of the polyamide resin particles in the resin composition containing particles can be adjusted to a moderate range, and the interlaminar fracture toughness, CAI and flexural modulus can be improved.
For the melting point of the polyamide 6/12 resin particles, it is preferable to be 170° C. to 220° C., it is more preferable to be 175° C. to 220° C., and it is still more preferable to be 180° C. to 205° C. from the viewpoint of moderately suppressing the polyamide 6/12 resin particles melting and entering the reinforcing fiber layer during the preparation of a fiber-reinforced composite material. In the embodiment, the melting point of the polyamide resin particles is found by increasing the temperature at a rate of 10° C./minute from 25° C. using a differential scanning calorimeter (DSC) and measuring the temperature of the top of the resulting endothermic peak. In the case where there are a plurality of endothermic peaks, the temperature of the top of the peak of the largest absorption of heat is taken as the melting point.
As the polyamide 6/12 resin particles used in the embodiment, commercially available products may be used; and examples include Orgasol 3202 D (registered trademark, manufactured by ARKEMA K.K.).
As the average particle size of the polyamide 6/12 resin particles mentioned above, 5 to 50 μm are preferable and 10 to 30 μm are more preferable from the viewpoint of controlling the thickness of the surface layer.
In the embodiment, for the amounts of the (A) component and the (B) component contained in the resin composition 2, when it is assumed that the total amount of the (A) component and the (B) component is 100 parts by mass, it is preferable that the amount of the (A) component be 65 to 78 parts by mass and the amount of the (B) component be 22 to 35 parts by mass. When the proportion of the contained (A) component is less than 65 parts by mass, that is, when the proportion of the contained (B) component is more than 35 parts by mass, the elastic modulus and the water resistance of the resulting fiber-reinforced composite tend to be reduced and the glass transition temperature of the resin cured substance tends to be reduced.
For the amount of the (C) component contained in the resin composition 2, when it is assumed that the total amount of the (A) component and the (B) component is 100 parts by mass, it is preferable to be 5 to 20 parts by mass and it is more preferable to be 7 to 15 parts by mass. If the amount of the contained (C) component is less than 5 parts by mass, it tends to be difficult to sufficiently increase the interlaminar fracture toughness, CAI and flexural modulus in the fiber-reinforced composite material; and in the case of more than 20 parts by mass, mechanical properties such as the glass transition temperature of the cured substance tend to be reduced.
In the embodiment, for the amounts of the (A) component and the (B) component contained in the surface layers 6a and 6b, when it is assumed that the total amount of the (A) component and the (B) component is 100 parts by mass, it is preferable that the amount of the (A) component be 65 to 78 parts by mass and the amount of the (B) component be 22 to 35 parts by mass. If the proportion of the contained (A) component is less than 65 parts by mass, that is, if the proportion of the contained (B) component is more than 35 parts by mass, the elastic modulus and the water resistance of the resulting fiber-reinforced composite tend to be reduced and the glass transition temperature of the resin cured substance tends to be reduced.
For the amount of the (C) component contained in the surface layers 6a and 6b, when it is assumed that the total amount of the (A) component and the (B) component is 100 parts by mass, it is preferable to be 5 to 20 parts by mass and it is more preferable to be 7 to 15 parts by mass. If the amount of the contained (C) component is less than 5 parts by mass, it tends to be difficult to sufficiently increase the CAI and the flexural modulus in the fiber-reinforced composite material; and in the case of more than 20 parts by mass, mechanical properties such as the glass transition temperature of the cured substance tend to be reduced.
For the amount of the (D) component contained in the surface layers 6a and 6b, when it is assumed that the total amount of the (A) component and the (B) component is 100 parts by mass, it is preferable to be 15 to 45 parts by mass and it is more preferable to be 25 to 40 parts by mass. If the amount of the contained (D) component is less than 15 parts by mass, it tends to be difficult to sufficiently increase the interlaminar fracture toughness, CAI and flexural modulus in the fiber-reinforced composite material; and in the case of more than 45 parts by mass, the flexural modulus tends to be reduced. In the embodiment, it is preferable that the total amount of the (D1) component and the (D2) component contained be in the range mentioned above.
Regarding the blending ratio of the (D1) component and the (D2) component, it is preferable that the amount of the (D2) component be 10 to 1000 parts by mass, it is more preferable that the above amount be 20 to 500 parts by mass, and it is still more preferable that the above amount be 30 to 300 parts by mass, with respect to 100 parts by mass of the (D1) component, from the viewpoint of sufficiently increasing the CAI and interlaminar fracture toughness.
The surface layers 6a and 6b in the prepreg of the embodiment refer to between the prepreg surface and the reinforcing fibers of the reinforcing fiber layer, and the amount mentioned above of the (D) component contained in the surface layer can be calculated on the basis of, for example, the amounts of the (A) component, the (B) component, and the (C) component contained detected between the prepreg surface and the reinforcing fibers of the reinforcing fiber layer.
In the prepreg of the embodiment, another component such as (E) a toughness improver may be blended to the surface layer and the reinforcing fiber layer to the extent that their physical properties are not impaired. Examples of (E) the toughness improver include phenoxy resins “YP-70”, “YP-50”, and “FZ-316” (registered trademark, all manufactured by NIPPON STEEL & SUMIKIN CHEMICAL CO., LTD.); and a polyethersulfone “SUMIKAEXCEL PES” (registered trademark, manufactured by Sumitomo Chemical Company, Limited).
As still another component, a nanocarbon, a fire retardant, a mold release agent, etc. may be blended. Examples of the nanocarbon include carbon nanotubes, fullerene, and derivatives of each of them. Examples of the fire retardant include red phosphorus, phosphoric acid esters such as triphenyl phosphate, tricresyl phosphate, trixylenyl phosphate, cresyl diphenyl phosphate, xylenyl diphenyl phosphate, resorcinol bis(phenyl phosphate), and bisphenol A bis(diphenyl phosphate), and boric acid esters. Examples of the mold release agent include silicon oil, stearic acid esters, and carnauba wax.
As the reinforcing fibers in the embodiment, glass fibers, carbon fibers, graphite fibers, aramid fibers, boron fibers, alumina fibers, silicon carbide fibers, and the like may be used. Two or more of these fibers may be mixed for use. It is preferable to use carbon fibers or graphite fibers and it is more preferable to use carbon fibers in order to obtain a molded product that is lighter in weight and higher in durability.
As the carbon fibers used in the embodiment, either of PAN-based carbon fibers and pitch-based carbon fibers may be used.
In the embodiment, any type of carbon fibers or graphite fibers may be used in accordance with the use. For the tensile elastic modulus in a strand tensile test of the carbon fibers or the graphite fibers, it is preferable to be 150 to 650 GPa, it is more preferable to be 200 to 550 GPa, and it is still more preferable to be 230 to 500 GPa because a composite material that is excellent in impact resistance and has high rigidity and mechanical strength can be obtained. The strand tensile test refers to a test performed on the basis of HS R 7601 (1986) after carbon fibers or graphite fibers in a bundle form are impregnated with an epoxy resin and curing is performed at a temperature of 130° C. for 35 minutes.
The form of the reinforcing fibers in the prepreg and the fiber-reinforced composite material of the embodiment is not particularly limited; for example, long fibers uniformly extended in one direction, rattans, textiles, mats, knits, braids, short fibers chopped to a length of less than 10 mm, and the like may be used. Here, the long fiber(s) refers to a single fiber or a fiber bundle substantially continuous for 10 mm or more. The short fiber(s) refers to a fiber bundle cut to a length of less than 10 mm. For uses in which it is required for the specific strength and the specific elastic modulus to be high, an arrangement in which a reinforcing fiber bundle is uniformly extended in one direction like the prepreg of the embodiment is most suitable; but also an arrangement of a cloth (textile) form, which is easy to handle, can be used.
In the prepreg of the embodiment, for the amount of reinforcing fibers per unit area, it is preferable to be 25 to 3000 g/m2. If the amount of reinforcing fibers is less than 25 g/m2, it is necessary to increase the number of stacked sheets in order to obtain a prescribed thickness during molding a fiber-reinforced composite material, and operation may be complicated. On the other hand, if the amount of reinforcing fibers is more than 3000 g/m2, the draping properties of the prepreg tend to be poor. When the prepreg is a flat surface or a simple curved surface, the amount of reinforcing fibers may be more than 3000 g/m2. The percentage of contained fibers in the prepreg is preferably 30 to 90 mass %, more preferably 35 to 85 mass %, and still more preferably 40 to 80 mass %. If the content percentage is less than 30 mass %, the amount of the resin is too large; and the advantage of a fiber-reinforced composite material excellent in specific strength and specific elastic modulus may not be obtained, or during the molding of a fiber-reinforced composite material, the amount of heat generated during curing may be too large. If the content percentage is more than 90 mass %, an impregnation defect of the resin occurs and the resulting composite material tends to include a large amount of voids.
Next, production methods for prepregs according to one embodiment of the present invention are described.
In the method shown in
The prepreg 12 of
Each resin composition with which the reinforcing fiber bundle is impregnated can be prepared by kneading the (A) to (C) components mentioned above and, as necessary, other components, or the (A) to (D) components mentioned above and, as necessary, other components.
The method for kneading a resin composition is not particularly limited; for example, a kneader, a planetary mixer, a biaxial extruder, etc. are used. It is preferable that, from the viewpoint of the dispersibility of the particle components of the (D) component etc., the particles be diffused into liquid resin components beforehand with a homomixer, three rolls, a ball mill, a bead mill, ultrasonic waves, and the like. Furthermore, during mixing with a matrix resin, during preliminary diffusion of particles, or in other cases, it is possible to perform heating or cooling, or pressurization or depressurization, as necessary. After kneading, immediate storage in a refrigerator or a freezer is preferable from the viewpoint of storage stability.
As the viscosity of the resin composition, 10 to 20000 Pa·s at 50° C. are preferable from the viewpoint of the production of a precursor film. 10 to 10000 Pa·s are more preferable, and 50 to 6000 Pa·s are most preferable. In the case of less than 10 Pa·s, the tackiness of the resin composition may be increased, and coating may be difficult. In the case of more than 20000 Pa·s, semisolidification occurs and coating is difficult.
Examples of the method for impregnating fibers with a resin composition include the wet method in which a resin composition is dissolved in a solvent such as methyl ethyl ketone or methanol to be reduced in viscosity and impregnation therewith is performed and the hot melt method (dry method) in which the viscosity is reduced by heating and impregnation is performed.
The wet method is a method in which reinforcing fibers are immersed in a solution of a resin composition and then pulled up and the solvent is vaporized using an oven or the like. The hot melt method is a method in which reinforcing fibers are directly impregnated with a resin composition that has been reduced in viscosity by heating or a method in which a resin composition is once applied onto a mold release paper sheet or the like in a coating manner to fabricate a film, subsequently the film is superposed from both sides or one side of reinforcing fibers, and heating and pressurization are performed to impregnate the reinforcing fibers with the resin. The hot melt method is preferable because there is substantially no solvent remaining in the prepreg.
The prepreg according to the embodiment can be made into a fiber-reinforced composite material by a method in which, after stacking, the resin is cured by heating while pressure is applied to the stacked matter or other methods. Here, examples of the method for applying heat and pressure include the press molding method, the autoclave molding method, the bagging molding method, the wrapping tape method, and the internal pressure molding method. The wrapping tape method is a method in which a prepreg is wound around a cored bar such as a mandrel and a tubular body made of a fiber-reinforced composite material is molded, and is a method suitable in fabricating stick-like bodies such as golf shafts and fishing rods. More specifically, it is a method in which a prepreg is wound around a mandrel, a wrapping tape formed of a thermoplastic film is wound on the outside of the prepreg in order to fix and apply pressure to the prepreg, the resin is cured by heating in an oven, and then the cored bar is taken out to obtain a tubular body.
The internal pressure molding method is a method in which a preform in which a prepreg is wound around an internal pressure applier such as a tube made of a thermoplastic resin is set in a mold, and subsequently a high pressure gas is introduced into the internal pressure applier to apply pressure and at the same time the mold is heated to perform molding. This method is preferably used in molding complicated shaped objects such as golf shafts, bats, and rackets for tennis, badminton, etc.
A resin composition containing particles that contains the (A) to (D) components mentioned above and, as necessary, other components can be suitably used for the preparation of the prepreg described above.
A resin composition containing particles in which the amount of the contained (D) component is 15 to 45 parts by mass and preferably 25 to 40 parts by mass when it is assumed that the total amount of the (A) component and the (B) component is 100 parts by mass can be suitably used as the material for forming the surface layer of the prepreg. For the resin composition containing particles, it is preferable that the glass transition temperature of its cured substance obtained by increasing the temperature at a temperature increase rate of 2.0° C./minute from room temperature to 185° C. and then performing curing under the conditions of the same temperature and 2 hours be 190° C. or more.
It is preferable that the temperature at which the stacked matter mentioned above is heated to cure the resin be 160 to 190° C., it is more preferable that the above temperature be 170 to 190° C., and it is still more preferable that the above temperature be 180 to 190° C., from the viewpoint of moderately melting the PA 12 resin particles and moderately suppressing the PA 6/12 resin particles melting and entering the reinforcing fiber layer. Here, the temperature at which the stacked matter mentioned above is heated to cure the resin refers to the temperature of the prepreg.
The retention time at the temperature at which the stacked matter mentioned above is heated to cure the resin can be 30 minutes to 10 hours, and is preferably 1 to 6 hours.
The temperature increase rate to the heating temperature mentioned above can be selected arbitrarily, but it is preferable to perform at 0.3 to 3° C./minute from the viewpoint of productivity.
It is preferable that the pressure in the heating mentioned above be 0.2 to 1.0 MPa, and it is more preferable that the above pressure be 0.3 to 0.8 MPa.
After curing by heating, the temperature can be decreased at a rate of −0.3 to −3.0° C./minute.
Thus, a fiber-reinforced composite material can be obtained.
In the fiber-reinforced composite material, for the volume proportion of C1 in the total amount of the amount C1 of the polyamide resin contained in the resin cured substance between reinforcing fiber layers and the amount C2 of the polyamide resin contained in the reinforcing fiber layers, {C1/(C1+C2)}×100, it is preferable to be 70 volume % or more and it is more preferable to be 80 volume % or more.
The amount of the contained polyamide resin is found by analyzing, by microscopic observation, a cross section of the fiber-reinforced composite material taken along a plane orthogonal to the direction in which an arbitrary reinforcing fiber in the fiber-reinforced composite material extends and performing image analysis to observe the distribution of the polyamide resin.
The fiber-reinforced composite material according to the embodiment can be obtained also by directly impregnating a reinforcing fiber matrix with a resin composition and performing curing. For example, the production can be performed by a method in which a reinforcing fiber matrix is placed in a mold and then a resin composition containing the (A) to (D) components mentioned above is poured in followed by impregnation and curing, or a method in which a reinforcing fiber matrix and a film formed of a resin composition containing the (A) to (D) components mentioned above are stacked and the stacked body is heated and pressurized. The film mentioned above can be obtained by applying a prescribed amount of a resin composition with a uniform thickness onto a mold release paper sheet or a mold release film beforehand. Examples of the reinforcing fiber matrix include long fibers uniformly extended in one direction, bidirectional textiles, unwoven fabrics, mats, knits, and braids. The stacking herein includes not only the case where fiber matrices are simply superposed but also the case where preforming is performed by attachment to various molds or core materials. As the core materials, foam cores, honeycomb cores, and the like are preferably used. As the foam cores, urethanes and polyimides are preferably used. As the honeycomb cores, aluminum cores, glass cores, aramid cores, and the like are preferably used.
In the fiber-reinforced composite material according to the embodiment, for the compressive strength after impact (CM) measured in accordance with ASTM D7136 and D7137, it is preferable to be 210 MPa or more and it is more preferable to be 220 MPa or more.
In the fiber-reinforced composite material according to the embodiment, for the mode I interlaminar fracture toughness value (G1c) measured in accordance with ASTM D5528, it is preferable to be 250 J/m2 or more and it is more preferable to be 260 J/m2 or more.
In the fiber-reinforced composite material according to the embodiment, for the mode II interlaminar fracture toughness value (G2c) measured in accordance with Composite Materials Handbook 17-1, it is preferable to be 1500 J/m2 or more and it is more preferable to be 1800 J/m2 or more.
In the fiber-reinforced composite material according to the embodiment, for the glass transition temperature of the resin cured substance, it is preferable to be 180° C. or more and it is more preferable to be 190° C. or more.
The fiber-reinforced composite material according to the embodiment having the physical properties mentioned above is suitably used for railroad vehicles, aircraft, building members, and other general industrial uses.
The present invention will now be specifically described using
Examples, but the present invention is not limited to them. The measurements of various physical properties are based on the following methods. The results are shown in Table 1.
For Examples and Comparative Examples, the source materials were mixed with heating at the ratios shown in Table 1, and a first resin composition containing no particles (the “first” composition in Table) and a second resin composition containing particles (the “second” composition in Table) were obtained. The source materials used here are as follows.
The (A) component: a benzoxazine resin
F-a: a bisphenol F-aniline type (F-a type benzoxazine, manufactured by SHIKOKU CHEMICALS CORPORATION)
P-a: a phenol-aniline type (P-a type benzoxazine, manufactured by SHIKOKU CHEMICALS CORPORATION)
The (B) component: an epoxy resin 2021P: “CELLOXIDE” (registered trademark) 2021P (manufactured by Daicel Chemical Industries, Ltd.)
The (C) component: a curing agent
BPF (9,9-bis(4-hydroxyphenyl)fluorene, manufactured by Osaka Gas Chemicals Co., Ltd.)
The (D) component: polyamide resin particles
The (D1) component
PA 12 (1): polyamide 12 resin particles (VESTOSINT 2158, average particle size: 20 μm, manufactured by Daicel-Evonik Ltd.)
PA 12 (2): polyamide 12 resin particles (VESTOSINT 2159, average particle size: 10 μm, manufactured by Daicel-Evonik Ltd.)
The (D2) component
PA 6/12 (80/20): particles made of a polyamide 6/12 copolymer (a random copolymer) in which caprolactam and laurolactam are copolymerized at a molar ratio of 80:20, (average particle size: 20 μm)
PA 6/12 (75/25): particles made of a polyamide 6/12 copolymer (a random copolymer) in which caprolactam and laurolactam are copolymerized at a molar ratio of 75:25, (average particle size: 20 μm)
PA 6/12 (90/10): particles made of a polyamide 6/12 copolymer (a random copolymer) in which caprolactam and laurolactam are copolymerized at a molar ratio of 90:10, (average particle size: 20 μm)
The (E) component: a toughness improver
YP 70: a phenoxy resin (YP-70, manufactured by NIPPON STEEL & SUMIKIN CHEMICAL CO., LTD.)
<Production of a Prepreg>
The first and second resin compositions obtained were each applied onto a mold release paper sheet at 70 to 100° C. to obtain a first resin film with 18 g/m2 and a second resin film with 25 g/m2. The first resin film obtained was supplied from the upper and lower sides of carbon fibers uniformly extended in one direction and the space between fibers was impregnated therewith to form a carbon fiber layer. Subsequently, the second resin film was laminated from the upper and lower sides of the carbon fiber layer to form surface layers; thus, a prepreg was prepared. The amount of carbon fibers per unit area of the prepreg was 150 g/m2, and the total amount of the resin composition in the carbon fiber layer and the surface layers (amount of matrix resin) was 86 g/m2.
<Measurement of the melting point of the polyamide resin particles>
The polyamide 12 resin particles and the polyamide 6/12 resin particles that are the (D) component mentioned above were increased in temperature at a rate of 10° C./minute from 25° C. using a differential scanning calorimeter (DSC), and the temperature of the top of the resulting endothermic peak was taken as the melting point of the polyamide resin particles. The melting point of the polyamide 12 resin particles was 184° C., the melting point of the polyamide 6/12 (80/20) resin particles was 194° C., the melting point of the polyamide 6/12 (75/25) resin particles was 187° C., and the melting point of the polyamide 6/12 (90/10) resin particles was 200° C.
<Measurement of the Melting Temperature of the Polyamide Resin Particles in the Second Resin Composition>
The second resin composition obtained was increased in temperature at a rate of 10° C./minute from 25° C. using a differential scanning calorimeter (DSC), and the temperature of the top of the resulting endothermic peak was taken as the melting temperature of the polyimide resin particles in the second resin composition. The results are shown in Table 1. In an example in which two melting temperatures are listed in the column of melting temperature in Table 1, the value in the upper side is the melting temperature of the (D1) component and the value in the lower side is the melting temperature of the (D2) component. A DSC chart of the second resin composition of Example 2 is shown in
<Measurement of the Glass Transition Temperature>
The second resin composition obtained was increased in temperature at a temperature increase rate of 2.0° C./minute from room temperature to 185° C. and cured for 2 hours at the same temperature in an oven to obtain a resin cured substance. For the cured substance obtained, the middle point temperature found on the basis of JIS K 7121 (1987) using a differential scanning calorimeter (DSC) was measured as the glass transition temperature. The results are shown in Table 1.
<Measurement of the Flexural Modulus>
The second resin composition obtained was increased in temperature at a temperature increase rate of 2.0° C./minute from room temperature to 185° C. and cured for 2 hours at the same temperature to obtain a resin cured substance having a thickness of 2 mm. For the resin cured substance, the flexural modulus was measured in accordance with HS J 7171. The results are shown in Table 1.
<Measurement of the CAI>
Prepregs obtained were stacked 32 plies (layers) pseudo-isotropically with a configuration of [+45°/0°/−45°/90°]4s, were increased in temperature in an autoclave at a temperature increase rate of 2.0° C./minute from room temperature to 185° C. at a pressure of 0.6 MPa, and were then cured by heating for 2 hours at the same temperature; thus, a fiber-reinforced composite material was obtained. From the fiber-reinforced composite material, a sample of 150 mm long×100 mm broad was cut out in accordance with ASTM D7136 and D7137, and a falling weight impact of 6.7 J/mm was applied to a central portion of the sample; thus, the compressive strength after impact (CAI) was found. The results are shown in Table 1.
<Mode I Interlaminar Fracture Toughness Test (G1c)>
Prepregs obtained were stacked 26 plies with each carbon fiber arranged so as to extend in the same direction, and a Kapton film (1 mil) (manufactured by DU PONT-TORAY CO., LTD.) was interposed in a partial region of the central interlayer (between the 13th layer and 14th layer) so as to introduce a precrack on the side surface of the stacked body perpendicular to the direction of the carbon fibers. Here, 1 mil means 1/1000 inches or 25.3995 μm. This was increased in temperature in an autoclave at a temperature increase rate of 2.0° C./minute from room temperature to 185° C. at a pressure of 0.6 MPa, and was then cured by heating for 2 hours at the same temperature; thus, a fiber-reinforced composite material was obtained. From the fiber-reinforced composite material, a sample of 264.0 mm long (fiber direction)×25.4 mm broad was cut out, and a hinge was bonded to each edge portion to obtain a test piece. This test piece was subjected to a double cantilever beam test at a loading speed of 1.0 mm/min in accordance with ASTM D5528 to find the mode I interlaminar fracture toughness value (G1c). The results are shown in Table 1.
<Mode II interlaminar fracture toughness test (G2c)>
Prepregs obtained were stacked 26 plies with each carbon fiber arranged so as to extend in the same direction, and a Kapton film (1 mil) (manufactured by DU PONT-TORAY CO., LID.) was interposed in a partial region of the central interlayer (between the 13th layer and 14th layer) so as to introduce a precrack on the side surface of the stacked body perpendicular to the direction of the carbon fibers. Here, 1 mil means 1/1000 inches or 25.3995 μm. This was increased in temperature in an autoclave at a temperature increase rate of 2.0° C./minute from room temperature to 185° C. at a pressure of 0.6 MPa, and was then cured by heating for 2 hours at the same temperature; thus, a fiber-reinforced composite material was obtained. From the fiber-reinforced composite material, a sample of 264.0 mm long (fiber direction)×25.4 mm broad was cut out to obtain a test piece. This test piece was subjected to an end-notched flexure test at a loading speed of 1.0 mm/min in accordance with Composite Materials Handbook 17-1 to find the mode II interlaminar fracture toughness value (G2c). The results are shown in Table 1.
<The Abundance Ratio (volume %) of the Polyamide Resin Between Carbon Fiber Layers>
A cross section of the fiber-reinforced composite material taken along a plane orthogonal to the direction in which an arbitrary carbon fiber in the fiber-reinforced composite material obtained in the measurement of CAI extends was analyzed by microscopic observation (500 times), and image analysis was performed for a range of 500 μm×100 μm to observe the distribution of polyamide particles; thereby, the amount C1 of the polyamide resin contained in one piece of the resin cured substance between carbon fiber layers and the amount C2 of the polyamide resin contained in one carbon fiber layer were calculated. This measurement was performed on arbitrary 5 places that are combinations of different carbon fiber layers and different pieces of the resin cured substance, and the average value of the 5 places of C1 and C2 was used to find the volume proportion of C1, {C1/(C1+C2)}×100, per prepreg. The results are shown in Table 1.
<Evaluation at Various Temperature Increase Rates>
For CAI, G1c, and G2c, evaluation was further performed in the same way as described above except that the temperature increase rate was changed to 0.3° C./minute. The results are shown in Table 2 in combination with the evaluation results in the case of 2.0° C./minute.
As shown in Table 1, it has been found that, in Examples 1 to 5 in which two types of the specific polyamide resin particles were used, G1c, G2c, CAI, and flexural modulus can be achieved at a high level at the same time, and also the glass transition temperature of the resin material can be kept high.
Further as shown in Table 2, in Examples 1 to 5 in which two types of the specific polyamide resin particles were used, CAI, G1c, and G2c can be obtained at a high level stably even in the case of different temperature increase conditions in heating a stacked body of prepregs.
As a result of observation of cross-sectional photographs of the fiber-reinforced composite materials of Examples 1 to 5 obtained under the respective conditions listed in Table 2, a resin cured layer containing a polyamide resin between the fiber layers was confirmed to be formed in a sufficient thickness under any of the conditions. This suggests that the prepregs of Examples 1 to 5 can provide a resin composition containing particles and a fiber-reinforced composite material which can deal with a wide range of production conditions and at the same time can achieve CM, G1c, and G2c at a high level stably.
As described above, according to the present invention, a prepreg that makes it possible to obtain a fiber-reinforced composite material that, while using a benzoxazine resin having excellent moisture resistance and heat resistance, can achieve interlaminar fracture toughness, CAI, and flexural modulus at high level at the same time and can also keep the glass transition temperature of the resin material high, a resin composition containing particles for obtaining the prepreg, and a fiber-reinforced composite material can be provided. The fiber-reinforced composite material mentioned above can be used for aircraft uses, vessel uses, automobile uses, sports uses, and other general industrial uses.
1 . . . reinforcing fibers, 2 . . . resin composition, 3 . . . reinforcing fiber layer, 4a . . . polyamide 12 resin particles, 4b polyamide 6/12 resin particles, 5 . . . resin composition, 6a, 6b . . . surface layer, 7 . . . reinforcing fiber bundle, 8 . . . resin cured substance, 10, 11 . . . prepreg, 100 . . . fiber-reinforced composite material.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2013-238894 | Nov 2013 | JP | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/JP2014/078626 | 10/28/2014 | WO | 00 |
