WO2018186360A1 - 繊維強化複合体用芯材、及びそれを用いた繊維強化複合体 - Google Patents
繊維強化複合体用芯材、及びそれを用いた繊維強化複合体 Download PDFInfo
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- WO2018186360A1 WO2018186360A1 PCT/JP2018/014149 JP2018014149W WO2018186360A1 WO 2018186360 A1 WO2018186360 A1 WO 2018186360A1 JP 2018014149 W JP2018014149 W JP 2018014149W WO 2018186360 A1 WO2018186360 A1 WO 2018186360A1
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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
- C08J9/00—Working-up of macromolecular substances to porous or cellular articles or materials; After-treatment thereof
- C08J9/22—After-treatment of expandable particles; Forming foamed products
- C08J9/228—Forming foamed products
- C08J9/232—Forming foamed products by sintering expandable particles
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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
- C08J9/00—Working-up of macromolecular substances to porous or cellular articles or materials; After-treatment thereof
- C08J9/16—Making expandable particles
- C08J9/18—Making expandable particles by impregnating polymer particles with the blowing agent
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B5/00—Layered products characterised by the non- homogeneity or physical structure, i.e. comprising a fibrous, filamentary, particulate or foam layer; Layered products characterised by having a layer differing constitutionally or physically in different parts
- B32B5/22—Layered products characterised by the non- homogeneity or physical structure, i.e. comprising a fibrous, filamentary, particulate or foam layer; Layered products characterised by having a layer differing constitutionally or physically in different parts characterised by the presence of two or more layers which are next to each other and are fibrous, filamentary, formed of particles or foamed
- B32B5/24—Layered products characterised by the non- homogeneity or physical structure, i.e. comprising a fibrous, filamentary, particulate or foam layer; Layered products characterised by having a layer differing constitutionally or physically in different parts characterised by the presence of two or more layers which are next to each other and are fibrous, filamentary, formed of particles or foamed one layer being a fibrous or filamentary layer
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B7/00—Layered products characterised by the relation between layers; Layered products characterised by the relative orientation of features between layers, or by the relative values of a measurable parameter between layers, i.e. products comprising layers having different physical, chemical or physicochemical properties; Layered products characterised by the interconnection of layers
- B32B7/02—Physical, chemical or physicochemical properties
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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
- C08J9/00—Working-up of macromolecular substances to porous or cellular articles or materials; After-treatment thereof
- C08J9/04—Working-up of macromolecular substances to porous or cellular articles or materials; After-treatment thereof using blowing gases generated by a previously added blowing agent
- C08J9/06—Working-up of macromolecular substances to porous or cellular articles or materials; After-treatment thereof using blowing gases generated by a previously added blowing agent by a chemical blowing agent
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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
- C08J9/00—Working-up of macromolecular substances to porous or cellular articles or materials; After-treatment thereof
- C08J9/22—After-treatment of expandable particles; Forming foamed products
- C08J9/228—Forming foamed products
-
- C—CHEMISTRY; METALLURGY
- C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
- C08L—COMPOSITIONS OF MACROMOLECULAR COMPOUNDS
- C08L71/00—Compositions of polyethers obtained by reactions forming an ether link in the main chain; Compositions of derivatives of such polymers
- C08L71/08—Polyethers derived from hydroxy compounds or from their metallic derivatives
- C08L71/10—Polyethers derived from hydroxy compounds or from their metallic derivatives from phenols
- C08L71/12—Polyphenylene oxides
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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
- C08J2201/00—Foams characterised by the foaming process
- C08J2201/02—Foams characterised by the foaming process characterised by mechanical pre- or post-treatments
- C08J2201/034—Post-expanding of foam beads or sheets
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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
- C08J2203/00—Foams characterized by the expanding agent
- C08J2203/02—CO2-releasing, e.g. NaHCO3 and citric acid
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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
- C08J2203/00—Foams characterized by the expanding agent
- C08J2203/06—CO2, N2 or noble gases
-
- 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
- C08J2371/00—Characterised by the use of polyethers obtained by reactions forming an ether link in the main chain; Derivatives of such polymers
- C08J2371/08—Polyethers derived from hydroxy compounds or from their metallic derivatives
- C08J2371/10—Polyethers derived from hydroxy compounds or from their metallic derivatives from phenols
- C08J2371/12—Polyphenylene oxides
-
- 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
- C08J2425/00—Characterised by the use of homopolymers or copolymers of compounds having one or more unsaturated aliphatic radicals, each having only one carbon-to-carbon double bond, and at least one being terminated by an aromatic carbocyclic ring; Derivatives of such polymers
- C08J2425/02—Homopolymers or copolymers of hydrocarbons
- C08J2425/04—Homopolymers or copolymers of styrene
- C08J2425/06—Polystyrene
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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
- C08J9/00—Working-up of macromolecular substances to porous or cellular articles or materials; After-treatment thereof
- C08J9/0061—Working-up of macromolecular substances to porous or cellular articles or materials; After-treatment thereof characterized by the use of several polymeric components
-
- 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
- C08J9/00—Working-up of macromolecular substances to porous or cellular articles or materials; After-treatment thereof
- C08J9/04—Working-up of macromolecular substances to porous or cellular articles or materials; After-treatment thereof using blowing gases generated by a previously added blowing agent
- C08J9/12—Working-up of macromolecular substances to porous or cellular articles or materials; After-treatment thereof using blowing gases generated by a previously added blowing agent by a physical blowing agent
Definitions
- the present invention relates to a core material for a fiber-reinforced composite that is lightweight and has excellent processability when combined with a fiber reinforced layer or the like.
- fiber reinforced synthetic resin reinforced with fibers is lightweight and has high mechanical strength, in recent years, light weight and high mechanical strength are required in the automotive field, ship field, aviation field, medical field, etc. The use is expanding in the fields that are being used.
- Patent Document 3 discloses a polypropylene (PP) resin foam or a composite of a polymethacrylimide (PMI) resin foam and a fiber-reinforced composite material. The rigidity was low, and the composite conditions with the fiber reinforcement were limited.
- PP polypropylene
- PMI polymethacrylimide
- the polymethacrylimide (PMI) resin foam is excellent in heat resistance, since its production method is special, the shape of the foam is limited to a flat plate, and the desired shape cannot be obtained. There were also problems with poor appearance.
- the present inventors have found a core material that is excellent in workability when combined with a fiber reinforcing material by using a resin having a specific high temperature characteristic, and have made the present invention.
- the present invention is as follows.
- thermoplastic resin contains a thermoplastic resin, has a thermal shrinkage starting temperature of 80 ° C. or higher, a linear expansion coefficient of 10 ⁇ 10 ⁇ 5 mm / mm ⁇ ° C. or lower, and a heating dimensional change rate at 130 ° C. of ⁇ 4.
- a core material for a fiber-reinforced composite comprising a bead foam molded body of 0 to 0%.
- thermoplastic resin contains 30 to 75% by mass of a polyphenylene ether resin.
- thermoplastic resin 3% by mass or less with respect to 100% by mass of the thermoplastic resin. Core material.
- a fiber reinforcement characterized in that a skin material containing a fiber and a resin is disposed on at least a part of the surface of the core material for a fiber-reinforced composite according to any one of (1) to (5) Complex.
- the core material for a fiber reinforced composite of the present invention is excellent in processability when combined with a fiber reinforced material.
- the present embodiment a mode for carrying out the present invention (hereinafter also referred to as “the present embodiment”) will be described in detail.
- the following embodiments are examples for explaining the present invention, and the present invention is not limited to the following embodiments, and various modifications can be made within the scope of the gist of the present invention.
- the core material for a fiber-reinforced composite according to the present embodiment includes a bead foam molded body, and may consist only of a bead foam molded body.
- the core material may contain a member other than the bead foam molded body depending on the purpose and application.
- the bead foam molded body includes a thermoplastic resin, and optionally includes a trace amount of gas, an additive, and the like.
- the content of the thermoplastic resin in the bead foam molded body is preferably 50 to 100% by mass, and may be a bead foam molded body made of only a thermoplastic resin.
- the thermoplastic resin is not particularly limited, and the temperature at which the loss tangent tan ⁇ is maximum at 70 ° C. to 200 ° C. is Tp, and the storage elastic modulus (G′1) at (Tp ⁇ 30) ° C. and the storage elasticity at 150 ° C.
- the ratio (G′2 / G′1) of the rate (G′2) is preferably 0.25 to 0.95.
- G′2 / G′1 is more preferably 0.30 to 0.90, still more preferably 0.30 to 0.85.
- the thermoplastic resin preferably contains a polyphenylene ether resin from the viewpoint of adhesiveness to the fiber reinforcement, and may further contain a resin (other resin) other than the polyphenylene ether resin.
- the polyphenylene ether resin refers to a polymer containing a repeating unit represented by the following general formula (1).
- the polyphenylene ether resin is not particularly limited.
- R 1 and R 2 are alkyl groups having 1 to 4 carbon atoms
- R 3 and R 4 are hydrogen atoms or alkyl groups having 1 to 4 carbon atoms.
- Polymers containing units are preferred.
- Polyphenylene ether resins may be used alone or in combination of two or more.
- the weight average molecular weight of the polyphenylene ether resin is preferably 20,000 to 60,000.
- the content of the polyphenylene ether (PPE) resin in the present embodiment is preferably 30 to 75% by mass, more preferably 100% by mass with respect to 100% by mass of the thermoplastic resin contained in the bead foam molded product. Is 35 to 65% by mass, more preferably 35 to 50% by mass. When the PPE content is 30% by mass or more, excellent heat resistance is easily obtained, and when the PPE content is 75% by mass or less, excellent workability is easily obtained.
- thermoplastic resins and the like for example, polyolefin resins such as polyethylene, polypropylene, EVA (ethylene-vinyl acetate copolymer); polyvinyl alcohol; polyvinyl chloride; polyvinylidene chloride; ABS (acrylonitrile).
- polyolefin resins such as polyethylene, polypropylene, EVA (ethylene-vinyl acetate copolymer); polyvinyl alcohol; polyvinyl chloride; polyvinylidene chloride; ABS (acrylonitrile).
- -Butadiene-styrene resin resin; AS (acrylonitrile-styrene) resin; polystyrene resin; methacrylic resin; polyamide resin; polycarbonate resin; polyimide resin; polyacetal resin; Styrene, polyvinyl chloride, polyurethane, polyester, polyamide, 1,2-polybutadiene, fluoroelastomer, etc .; polyamide, polyacetal, polyester, fluorine And the like are; thermoplastic engineering plastics.
- a modified and crosslinked resin may be used as long as the object of the present invention is not impaired.
- polystyrene resins are preferable from the viewpoint of compatibility. These may be used alone or in combination of two or more.
- polystyrene-based resin examples include homopolymers of styrene or styrene derivatives, copolymers having styrene and / or styrene derivatives as main components, and the like.
- the styrene derivative is not particularly limited. For example, o-methylstyrene, m-methylstyrene, p-methylstyrene, t-butylstyrene, ⁇ -methylstyrene, ⁇ -methylstyrene, diphenylethylene, chlorostyrene, bromostyrene. Etc.
- Examples of homopolymers of styrene or styrene derivatives include polystyrene, poly ⁇ -methyl styrene, polychlorostyrene, and the like.
- Examples of the copolymer having styrene and / or styrene derivative as a main component include, for example, styrene- ⁇ -olefin copolymer; styrene-butadiene copolymer; styrene-acrylonitrile copolymer; styrene-maleic acid copolymer; Styrene-maleic anhydride copolymer; styrene-maleimide copolymer; styrene-N-phenylmaleimide copolymer; styrene-N-alkylmaleimide copolymer; styrene-N-alkyl-substituted phenylmaleimide copoly
- a rubber component such as butadiene may be added to the polystyrene resin as necessary.
- the content of the rubber component is preferably 1.0 to 20% by mass and more preferably 3.0 to 18% by mass with respect to 100% by mass of the polystyrene resin.
- the content of the other resin in the present embodiment is preferably 25 to 70% by mass with respect to 100% by mass of the thermoplastic resin contained in the bead foam molded body, from the viewpoint of the workability of the foam. Preferably, the content is 35 to 65% by mass.
- the gas is included in the manufacturing process (described later) of the bead foam molded body. Although it does not specifically limit as gas, Air, a carbon dioxide gas, the various gas used as a foaming agent, an aliphatic hydrocarbon gas, etc. are mentioned. Specific examples of the aliphatic hydrocarbon gas include butane and pentane.
- the concentration (content) of the aliphatic hydrocarbon gas in the bead foam molded body is preferably 500 ppm by volume or less, more preferably 200 volumes, based on the volume of the bead foam molded body. ppm or less.
- the concentration (content) of the aliphatic hydrocarbon gas in the core material is preferably 500 ppm by volume or less, more preferably 200 ppm by volume or less, based on the volume of the core material. It is.
- the content of the aliphatic hydrocarbon gas can be measured by gas chromatography.
- the content of the aliphatic hydrocarbon gas is 500 ppm by volume or less, it becomes easy to suppress the expansion of the bead foam molded body due to heating at the time of compounding, so it becomes easy to obtain excellent surface smoothness, adhesiveness, and strength. Also, the reproducibility of the dimensions is good, and it becomes easy to suppress the back swelling. Moreover, it becomes easy to perform compounding with a more complicated shape such as a shape with a portion having a different thickness.
- additives include flame retardants, rubber components, antioxidants, heat stabilizers, lubricants, pigments, dyes, light resistance improvers, antistatic agents, impact modifiers, talc and other nucleating agents, glass beads , Inorganic fillers, anti-blocking agents and the like.
- the flame retardant examples include organic flame retardants such as halogen compounds such as bromine compounds, non-halogen compounds such as phosphorus compounds and silicone compounds; metal hydroxides represented by aluminum hydroxide and magnesium hydroxide, three And inorganic flame retardants such as antimony oxides and antimony compounds represented by antimony pentoxide.
- organic flame retardants such as halogen compounds such as bromine compounds, non-halogen compounds such as phosphorus compounds and silicone compounds
- metal hydroxides represented by aluminum hydroxide and magnesium hydroxide metal hydroxides represented by aluminum hydroxide and magnesium hydroxide
- three And inorganic flame retardants such as antimony oxides and antimony compounds represented by antimony pentoxide.
- the content of the flame retardant is preferably 3% by mass or less, more preferably 1% by mass or less with respect to 100% by mass of the thermoplastic resin.
- the content of the flame retardant is in this range, it becomes easier to maintain heat resistance and rigidity during composite processing, and good adhesiveness is easily exhibited.
- the dimensions of the resulting composite are closer to the desired dimensions, and the reproducibility of the dimensions tends to be better.
- the thermal shrinkage starting temperature of the bead foam molded body is 80 ° C. or higher. If the heat shrinkage start temperature is lower than 80 ° C., the bead foam molded body contained in the core material shrinks at an early stage when heated when combined with the fiber reinforcement, so that the fiber reinforcement cannot follow the change and wrinkles. Etc. occur and the appearance deteriorates. More preferably, it is 85 ° C. or higher.
- heat shrink start temperature can be measured by the method as described in the below-mentioned Example.
- the linear expansion coefficient of the bead foam molding is 10 ⁇ 10 ⁇ 5 mm / mm ⁇ ° C. or less.
- the linear expansion coefficient is greater than 10 ⁇ 10 ⁇ 5 mm / mm ⁇ ° C.
- the bead foam molded body contained in the core material expands during the heating process when combined with the fiber reinforcement, whereas the fiber reinforcement does not expand. Inability to follow, resin withering, wrinkles, etc. occur, the appearance deteriorates, and the adhesiveness also decreases. More preferably, it is 5 ⁇ 10 ⁇ 5 mm / mm ⁇ ° C. or less.
- a linear expansion coefficient can be measured by the method as described in the below-mentioned Example.
- the rate of change in dimensional heating at 130 ° C. of the bead foam molding is ⁇ 4.0 to 0%. Note that minus means contraction and plus means expansion. If the heating dimensional change rate is smaller than -4.0%, that is, the shrinkage rate is larger than 4.0%, the density of the bead foam molded body contained in the core material increases, and the lightening effect is reduced. Therefore, a desired dimension cannot be obtained, or the reproducibility of the dimension is lowered. If the shrinkage is further increased, the adhesion between the bead foam molded product and the fiber reinforcing material is deteriorated, the adhesiveness and appearance are deteriorated, and finally the bead foam molded product is melted so that a composite product cannot be obtained. .
- the heating dimensional change rate is greater than 0%, that is, when the bead foam molded body expands, it becomes difficult to reduce the thickness.
- the dimensional reproducibility is deteriorated, and it is impossible to combine in a complicated shape.
- unevenness occurs on the surface of the bead foam molded product, not only the surface smoothness of the composite is deteriorated, but also the adhesiveness thereof is lowered.
- it is -3.5 to 0%, more preferably -3.0 to 0%.
- the heating dimensional change rate at 130 ° C. can be measured by the method described in Examples described later.
- the expansion ratio of the bead foam molding is not particularly limited, but is preferably 1.5 cm 3 / g or more, more preferably 2 cm 3 / g or more, and 40 cm 3 / g or less. Is more preferable, and more preferably 25 cm 3 / g or less. Within this range, it is easy to maintain excellent heat resistance and high-temperature rigidity while taking advantage of weight reduction.
- the expansion ratio can be measured by the method described in Examples described later.
- the bead foam molded body can be obtained by a bead foaming method.
- a bead foam molded product since it is excellent in moldability and can be molded into various shapes, there is an advantage that the degree of freedom of design becomes wider when used for structural members such as members.
- the foamed beads used in the present invention can be obtained, for example, by containing (impregnating) a foaming agent in a thermoplastic resin (impregnation step) and foaming the resin component (foaming step), but are not limited thereto. is not.
- the method of adding the foaming agent to the base resin is not particularly limited, and a generally performed method can be applied.
- a method of containing a foaming agent a method using an aqueous medium using a suspension system such as water (suspension impregnation), or a method using a thermally decomposable foaming agent such as sodium deuterium hydrogen (foaming agent decomposition method)
- a method of bringing the gas into contact with the base resin in a gas phase under a high pressure atmosphere below the critical pressure (gas phase) Impregnation) and the like a method of containing a foaming agent.
- the method of vapor phase impregnation in a high-pressure atmosphere below the critical pressure is particularly preferable.
- the method of impregnating in the gas phase has better solubility of the gas in the resin than the suspension impregnation carried out under a high temperature condition, and makes it easy to increase the content of the foaming agent. Therefore, it is easy to achieve a high expansion ratio, and the bubble size in the base resin is likely to be uniform.
- the blowing agent decomposition method is not only carried out under high temperature conditions, but not all of the added pyrolytic foaming agent becomes gas, so that the amount of gas generation tends to be relatively small. Therefore, the vapor phase impregnation has an advantage that the foaming agent content can be easily increased.
- facilities such as a pressure device and a cooling device are likely to be more compact, and the facility cost can be easily suppressed.
- the vapor phase impregnation conditions are not particularly limited, but the atmospheric pressure is preferably 0.5 to 6.0 MPa.
- the atmospheric temperature is preferably 5 to 30 ° C, more preferably 7 to 20 ° C.
- gas dissolution in the base resin is more likely to proceed more efficiently.
- the ambient temperature is low, the amount of impregnation increases, but the impregnation rate is slow, and if the ambient temperature is high, the amount of impregnation decreases, but the impregnation rate tends to increase. In order to proceed, it is preferable to set the above atmospheric temperature.
- a foaming agent is not specifically limited,
- the gas generally used can be used. Examples thereof include air, carbon dioxide gas, nitrogen gas, oxygen gas, ammonia gas, hydrogen gas, argon gas, helium gas, neon gas and other inorganic gases, trichlorofluoromethane (R11), dichlorodifluoromethane (R12), chlorodifluoromethane.
- R22 tetrachlorodifluoroethane (R112) dichlorofluoroethane (R141b) chlorodifluoroethane (R142b), difluoroethane (R152a), fluorocarbons such as HFC-245fa, HFC-236ea, HFC-245ca, HFC-225ca, propane, n -Saturated hydrocarbons such as butane, i-butane, n-pentane, i-pentane, neopentane, dimethyl ether, diethyl ether, methyl ethyl ether, isopropyl ether, n-butyl ether Ethers such as tellurium, diisopropyl ether, furan, furfural, 2-methylfuran, tetrahydrofuran, tetrahydropyran, dimethyl ketone, methyl ethyl ketone, diethyl ket
- Inorganic gas is preferred from the viewpoint of gas safety.
- the inorganic gas is less soluble in the resin than the organic gas such as hydrocarbon, and the gas is likely to escape from the resin after the foaming process or the molding process, so that there is an advantage that the dimensional stability of the molded product over time is further improved. Further, the plasticization of the resin by the residual gas hardly occurs, and there is an advantage that excellent heat resistance is easily expressed from an earlier stage after molding.
- carbon dioxide gas is preferable from the viewpoint of solubility in the resin and ease of handling, and the impregnation amount is preferably 0.5 to 10% by mass with respect to the resin. More preferably, the content is 1.0 to 9% by mass.
- the carbon dioxide impregnation amount is 0.5% by mass or more, it becomes easy to achieve a higher expansion ratio, the bubble size in the base resin is less likely to vary, and the variation in the expansion ratio among the base resins is reduced. It is a trend. When the amount is 10% by mass or less, the bubble size becomes appropriate, and the closed cell ratio tends to be easily maintained.
- the foaming method for foaming beads in the foaming process is not particularly limited.
- the foamed beads are released from a high-pressure condition in a low-pressure atmosphere at once, and the gas dissolved in the base resin is expanded or heated by pressurized steam.
- a method of expanding the gas dissolved in the base resin is particularly preferable. This is because the bubble size inside the base resin is likely to be uniform as compared with a method in which a low pressure atmosphere is opened from a high pressure condition.
- the introduction pressure of the steam supplied to the foaming machine is preferably 6.0 to 15.0 kg / cm 2 ⁇ G, more preferably 6.1 to 12.0 kg / cm 2 ⁇ G.
- the introduction pressure is low, the ability to heat the pre-foaming machine is low, so that the time required to raise the temperature to a predetermined temperature is long when pre-foaming is performed.
- a phenomenon called “blocking” in which the surface of the pre-expanded particles is once melted and integrated with the adjacent pre-expanded particles easily occurs.
- the vapor pressure in the pre-foaming machine rises rapidly, and it becomes easy to obtain good pre-foamed particles that are not blocked.
- the steam can be more uniformly and efficiently foamed by introducing the steam from a large number of steam holes from the bottom of the foaming furnace and stirring the resin with stirring blades.
- the rotation speed of the stirring blade is preferably 20 to 120 rpm, more preferably 50 to 90 rpm. If the rotational speed is 20 rpm or less, the pressurized water vapor does not hit uniformly and foaming control is difficult or problems such as blocking tend to occur. If it is 120 rpm or more, the foamed beads are damaged by the stirring blades. , The closed cell ratio tends to decrease, or the desired foaming ratio tends to be difficult to obtain.
- one-stage foaming may be performed, or multi-stage foaming including secondary foaming, tertiary foaming, or the like may be performed.
- multistage foaming there is an advantage that it is easy to prepare pre-expanded particles having a high expansion ratio.
- the gas used for the pressure treatment is not particularly limited as long as it is inert to the resin, but inorganic gases and hydrofluoroolefins having high gas safety and low gas global warming potential are preferred.
- the inorganic gas include air, carbon dioxide gas, nitrogen gas, oxygen gas, ammonia gas, hydrogen gas, argon gas, helium gas, and neon gas.
- the hydrofluoroolefin include HFO-1234y, HFO-1234ze (E) and the like can be mentioned, and air and carbon dioxide gas are particularly preferable from the viewpoint of ease of handling and economy.
- a technique for the pressure treatment is not particularly limited, and examples thereof include a technique of filling pre-expanded particles in a pressurized tank and supplying gas into the tank.
- the shape of the foam beads obtained in the foaming step is not particularly limited, and examples thereof include cylindrical, rectangular parallelepiped, spherical, and irregular pulverized products.
- the size (particle size) of the expanded beads is preferably 0.2 to 3 mm.
- the pre-foamed particles have an appropriate size and are easy to handle, and the filling during molding tends to be denser.
- size of a foam bead can be measured with a caliper.
- the expansion ratio of the expanded beads obtained in the foaming process are not particularly limited, preferably 1.5 ⁇ 40cm 3 / g, and more preferably 2 ⁇ 25cm 3 / g. Within this range, it becomes easy to obtain a bead foam molded article having excellent heat resistance and high-temperature rigidity while utilizing the advantages of weight reduction.
- the primary foaming magnification is preferably 1.4 to 10 cm 3 / g. Within this range, the cell size in the bead foam molded product tends to be uniform, and secondary foaming ability is easily imparted.
- the expansion ratio of the expanded beads refers to the ratio of the expanded beads volume Vp to the expanded beads weight Wp (Vp / Wp). Moreover, in this specification, the volume of a foam bead says the volume measured by the submergence method.
- a bead foam molding can be obtained (molding process) using a general molding method.
- foamed beads are filled in a mold and foamed by heating, and at the same time, the beads are fused together, and then solidified by cooling, and then molded.
- the filling method of the expanded beads is not particularly limited.
- a compression cracking method in which cracking is performed after filling with the compressed beads may be used.
- the pressure source for performing the pressure treatment is not particularly limited, but it is preferable to use an inorganic gas from the viewpoints of flame retardancy, heat resistance and dimensional stability described above.
- inorganic gas include air, carbon dioxide gas, nitrogen gas, oxygen gas, ammonia gas, hydrogen gas, argon gas, helium gas, neon gas, etc. From the viewpoint of ease of handling and economy, carbon dioxide gas and air are Although it is preferable, it is not limited thereto.
- the method of the pressure treatment is not particularly limited, and examples thereof include a method in which foaming beads are filled in a pressure tank and an inorganic gas is supplied into the tank to pressurize the tank.
- the foam beads are filled into the mold cavity under pressurized atmospheric pressure or reduced pressure, the mold is closed, and the mold cavity volume is reduced to 0 to Compressed so as to decrease by 70%, and then heated by supplying a heating medium such as steam into the mold, and heat-fused foam beads (for example, Japanese Patent Publication No. 46-38359), Expanding the foam beads with pressurized gas in advance to increase the pressure inside the foam beads, increasing the secondary foamability of the foam beads, and maintaining the secondary foamability while maintaining the secondary foam performance. Is filled in a mold cavity and the mold is closed, and then a heating medium such as steam is supplied into the mold and heated to heat and fuse the foam beads (for example, Japanese Patent Publication No. 51-22951). Molding)
- a heating medium such as steam is supplied into the cavities and heated, and the expanded beads It can also be molded by a compression filling molding method (Japanese Patent Publication No. 4-46217).
- a heating medium such as steam is then supplied. It can also be molded by a normal pressure filling molding method (Japanese Patent Publication No. 6-49795) or a combination of the above methods (Japanese Patent Publication No. 6-22919) or the like in which heating and fusing of foam beads are performed. .
- Expansion ratio of the molded article using the expanded beads of the present embodiment is not particularly limited, preferably 1.5 ⁇ 40cm 3 / g, and more preferably 2 ⁇ 25cm 3 / g. Within this range, it becomes easy to obtain a bead foam molded article having excellent heat resistance and high-temperature rigidity while utilizing the advantages of weight reduction.
- the expansion ratio of the bead foam molded body refers to the ratio (Vb / Wb) of the volume Vb of the bead foam molded body to the weight Wb of the bead foam molded body.
- the volume of a bead foam molding says the volume measured by the submergence method.
- Fiber reinforced composite Using the core material of the present embodiment, it can be combined with a fiber reinforcing material (for example, a skin material) to obtain a fiber reinforced composite.
- a fiber reinforcing material for example, a skin material
- the fiber reinforced composite is a composite in which a skin material containing fibers and resin is disposed on at least a part of the surface of the core material including the bead foam molded product.
- the core material may be a core material made only of a bead foam molded body.
- the portion on the surface of the core material where the skin material is disposed may be appropriately determined according to the shape of the core material. In the case of a lump, it may be the whole or part of the surface that can be seen from a specific direction in a stationary state. In the case of a line, the surface of a predetermined length in the extending direction from one end It may be all or part of.
- the skin material in the fiber-reinforced composite of the present embodiment includes fibers and a resin, and optionally includes additives and the like.
- fiber--- examples of the fiber include high-strength and high-modulus fiber, and specifically, carbon fiber, glass fiber, and organic fiber (for example, “Kevlar (registered trademark)” manufactured by DuPont, USA). Polyaramid fibers), alumina fibers, silicon carbide fibers, boron fibers, silicon carbide fibers and the like.
- those having a high specific elastic modulus which is a ratio of elastic modulus and density, specifically, carbon fibers and glass fibers are preferable, and carbon fibers are more preferable. These fibers may be used alone or in combination of two or more.
- the tensile elastic modulus of the fiber in the present embodiment measured in accordance with JIS-K7127, is preferably 200 to 850 GPa from the viewpoint of ensuring high rigidity.
- the fiber content in the present embodiment is preferably 40 to 80% by mass with respect to 100% by mass of the skin material.
- the rigidity, in terms of weight reduction, the surface of the skin material preferably 50 ⁇ 4000g / m 2, more preferably 100 ⁇ 1000g / m 2, for example, 200g / M 2 may be used.
- thermosetting resins examples include thermoplastic resins.
- thermosetting resins that are cured by external energy addition such as heat, light, and electron beam are preferable, and specifically, epoxy resins are preferable. These resins may be used alone or in combination of two or more.
- the glass transition temperature of the resin is preferably 80 to 250 ° C., more preferably 80 to 180 ° C., from the viewpoints of adhesion to the core material, deformation and warpage.
- the glass transition temperature can be measured by the midpoint method according to ASTM-D-3418.
- the resin is a thermosetting resin
- its curing temperature is preferably 80 to 250 ° C., more preferably 80 to 150 ° C., from the viewpoints of adhesion to the core material, deformation and warpage.
- the resin content in the present embodiment is preferably 20 to 60% by mass, more preferably 30 to 30% by mass with respect to 100% by mass of the skin material from the viewpoint of adhesiveness to the core material, deformation and warpage. 50% by mass.
- An example of the method for manufacturing a fiber reinforced composite in the present embodiment is a method for forming a fiber reinforced composite by adding a core material including a bead foam molded body and a skin material including a fiber and a resin to a molding machine. A way to get a body.
- the shape of the core material is not particularly limited and can be appropriately determined according to the purpose and application. Examples thereof include a molded product, a particle shape, a sheet shape, a linear shape (thread shape), and a lump shape.
- the fiber is immersed in the molten resin, or the molten resin is sprayed onto the fiber to impregnate the fiber with the resin to obtain the skin material.
- the skin material may be prepared as a cross prepreg. Note that after the resin is impregnated with fibers, the resin may be cured by light or heat.
- the shape of the fiber reinforced composite is also a sheet, it may be as described for the fiber reinforced composite of this embodiment.
- the core material for example, a bead foam molded body
- the skin material may be filled in a molding machine in a desired arrangement state and simultaneously molded.
- the bead foam molded body may be further foamed in the molding step.
- the sheet-like bead foam molded body is positioned between the two sheet-like skin materials. These may be filled into the molding machine.
- these are placed in the molding machine so that the lump bead foam molding is wrapped with the sheet skin material.
- these are filled into a molding machine so that the linear bead foam molding is wrapped with a sheet-like skin material. It's okay.
- the pressure is maintained at a temperature of 80 to 150 ° C., preferably 100 to 120 ° C. for 0 to 5 minutes, preferably 1 to 3 minutes without applying pressure, and thereafter 0 to 3 MPa.
- the pressure is preferably maintained at a pressure of 0.1 to 1 MPa and a temperature of 80 to 150 ° C., preferably 100 to 120 ° C. for 5 to 30 minutes, preferably 10 to 20 minutes.
- the apparent density of the fiber-reinforced composite of this embodiment is preferably 0.05 to 1 g / cm 3 .
- the apparent density of the fiber reinforced composite refers to the ratio (W / V) of the weight of the fiber reinforced composite to the volume V of the fiber reinforced composite.
- the dimensions of the fiber reinforced composite of this embodiment may be appropriately determined according to the purpose and application.
- the thickness of the skin material may be 0.1 to 2 mm.
- the evaluation method of the core material for fiber reinforced composite (bead foam molding) and the fiber reinforced composite is as follows.
- Thermal shrinkage start temperature A plate-shaped bead foam molded body of 300 mm ⁇ 100 mm ⁇ thickness 10 mm was allowed to stand for 24 hours in an environment adjusted to 23 ° C. Three 200 mm straight lines were drawn in parallel to this bead foam molded body at intervals of 20 mm, and the length (mm) of the line was measured with calipers. Thereafter, the length of the wire (mm) was measured after the bead foam molding was put into an oven at 30 ° C. for 2 hours and then left at 23 ° C. for 1 hour. This measurement was repeated by raising the oven temperature in increments of 5 ° C., and the temperature when all three lines were measured at 23 ° C. was taken as the heat shrinkage start temperature (° C.).
- linear expansion coefficient (dimension B ⁇ dimension C) / (dimension A ⁇ 35)
- Heating dimensional change rate at 130 ° C. Measurement was performed according to the dimensional stability test B method at high temperature of JIS K6767 except that the heating temperature was 130 ° C. and the heating time was 1.5 minutes. The heating time was 1.5 minutes after the temperature in the dryer reached 130 ° C. after the test piece was put into the hot air circulating dryer.
- Viscoelasticity measurement About the resin before foaming, viscoelasticity measurement was performed on the following conditions using ARES-G2 by TA Instruments. The measurement is performed while the temperature is lowered from 300 ° C., but when the resin is solidified and cannot be measured, data up to that temperature is used. From the obtained data, the temperature at which the loss tangent tan ⁇ reaches the maximum from 70 ° C. (when the measurement becomes impossible in the middle) to 200 ° C. is Tp, and the storage elastic modulus at (Tp-30) ° C. and 150 ° C. G′1 and G′2 were obtained, and G′2 / G′1 was calculated.
- the storage elastic modulus at the temperature at which measurement becomes impossible is defined as G′1.
- Measurement jig Cone and plate Measurement mode: Melting Sweep category: Temperature sweep Distortion amount: 10% Frequency: 10 rad / sec Temperature range: 70-300 ° C Temperature drop rate: 2 ° C / min Plate diameter: 25 ⁇ mm Gap interval: 1mm Automatic mode: Axial force ... 10g Sensitivity... 2.0g
- Residual gas concentration An appropriate amount of the bead foam molded body obtained in the examples and comparative examples was charged into a head space bottle and heated at a temperature equal to or higher than the softening point of the bead foam molded body sample. Thereafter, the gas in the headspace bottle was quantified by gas chromatography (manufactured by Shimadzu Corporation, GC14B). Helium (He) was used as a carrier gas and controlled in a constant flow rate mode (about 30 mL / min). In addition, the column (Porapak Q, 80/100 mesh, 3.2 mm ⁇ ⁇ 2.1 m) was heated and held at 50 to 150 ° C. and detected by a thermal conductivity type detector (TCD).
- TCD thermal conductivity type detector
- the volume of the aliphatic hydrocarbon gas was calculated from the detected area area and the calibration curve created with the standard gas sample. Then, the concentration (volume ppm) of the aliphatic hydrocarbon gas was calculated by dividing the volume of the aliphatic hydrocarbon gas by the volume of the bead foam molded product sample.
- Thickness The thickness (mm) of the fiber reinforced composites obtained in Examples and Comparative Examples and the thickness (mm) of the skin material were measured using calipers.
- Example 1 A cross prepreg composed of carbon fiber having a tensile modulus of 250 GPa and an epoxy resin having a curing temperature of 80 ° C. and having a fiber basis weight of 200 g / m 2 and a carbon fiber content of 60% by mass is used as a skin material. Two sheets were prepared. Further, 73% by mass of polyphenylene ether resin (PPE) and 12% by mass of impact-resistant polystyrene resin (HIPS) having a rubber concentration of 6% by mass (the content of the rubber component in the base resin is 0.6% by mass).
- PPE polyphenylene ether resin
- HIPS impact-resistant polystyrene resin
- Base resin pellets were prepared. When the viscoelasticity measurement of this base resin was implemented, Tp was 153 degreeC and G'2 / G'1 was 0.40. According to the method described in Example 1 of JP-A-4-372630, the base resin pellets are accommodated in a pressure-resistant container, the gas in the container is replaced with dry air, and then carbon dioxide (gas) is used as a blowing agent.
- PS general-purpose polystyrene resin
- the base resin pellet was impregnated with 7% by mass of carbon dioxide over 3 hours under conditions of a pressure of 3.2 MPa and a temperature of 11 ° C. Thereafter, the base resin pellets were foamed with pressurized steam while rotating the stirring blades at 77 rpm in a preliminary foaming machine to obtain foam beads.
- the foamed beads were pressurized to 0.5 MPa over 1 hour, then held at 0.5 MPa for 8 hours, and subjected to pressure treatment. This is filled into an in-mold molding die having water vapor holes, heated with pressurized steam to expand and fuse the foam beads together, cooled, taken out from the molding die, and 300 mm ⁇ 300 mm ⁇ 10 mm thick.
- a bead foam molded body (foam) having an expansion ratio of 10 cm 3 / g was obtained. It was 85 degreeC when the heat shrink start temperature of the obtained bead foaming molding was measured. When the linear expansion coefficient of the obtained bead foam molded product was measured, it was 5 ⁇ 10 ⁇ 5 mm / mm ⁇ ° C. The dimensional change rate at 130 ° C. of the obtained bead foam molding was ⁇ 3.6%. When the concentration of the aliphatic hydrocarbon gas in the obtained bead foam molded product was measured, it was below the detection limit (50 ppm by volume).
- the obtained bead foam molded product was used as a core material, and the skin material prepared as described above was laminated one by one on the upper and lower surfaces of the core material, and this laminate was then subjected to 3 at 100 ° C. without applying pressure. After holding for 1 minute, the skin material and the core material were simultaneously molded by holding for 15 minutes while pressing at a surface pressure of 0.4 MPa to obtain a fiber-reinforced composite. Details of the conditions are shown in Table 1. The appearance of the fiber reinforced composite of Example 1 was excellent without wrinkles or bubbles. Although there was a gap between the skin material and the core material, there was no problem in practical use. In addition, the dimensional reproducibility was at a level with no problem in actual use although there was some dimensional variation.
- Example 2 A polyphenylene ether-based resin (PPE) 40% by mass and a polystyrene-based resin (PS) 60% by mass were heated, melted and kneaded by an extruder, and then extruded to prepare a base resin pellet as a core material.
- PPE polyphenylene ether-based resin
- PS polystyrene-based resin
- the dimensional change rate at 130 ° C. of the obtained bead foam molded product was a shrinkage of 0.1% or less.
- concentration of the aliphatic hydrocarbon gas in the obtained bead foam molded product was measured, it was below the detection limit (50 ppm by volume).
- This was combined with a skin material in the same manner as in Example 1, and evaluated using the obtained fiber-reinforced composite. Details of the conditions are shown in Table 1.
- the fiber reinforced composite of Example 2 was excellent in appearance, adhesiveness, and dimensional reproducibility.
- Example 3 Using the thermoplastic resin of Example 2, a bead foam molded article having an expansion ratio of 5 cm 3 / g was produced. It was 95 degreeC when the heat shrink start temperature of the obtained bead foam molding was measured. When the linear expansion coefficient of the obtained bead foam molded product was measured, it was 4 ⁇ 10 ⁇ 5 mm / mm ⁇ ° C. The dimensional change rate at 130 ° C. of the obtained bead foam molded product was a shrinkage of 0.1% or less. When the concentration of the aliphatic hydrocarbon gas in the obtained bead foam molded product was measured, it was below the detection limit (50 ppm by volume). This was combined with a skin material in the same manner as in Example 1, and evaluated using the obtained fiber-reinforced composite. Details of the conditions are shown in Table 1. The fiber reinforced composite of Example 3 had excellent appearance, adhesiveness, and dimensional reproducibility as in Example 2.
- Example 4 Using the thermoplastic resin of Example 2, a bead foam molded article having an expansion ratio of 15 cm 3 / g was produced. It was 95 degreeC when the heat shrink start temperature of the obtained bead foam molding was measured. When the linear expansion coefficient of the obtained bead foam molded product was measured, it was 4 ⁇ 10 ⁇ 5 mm / mm ⁇ ° C. The dimensional change rate at 130 ° C. of the obtained bead foam molded product was a shrinkage of 0.1% or less. When the concentration of the aliphatic hydrocarbon gas in the obtained bead foam molded product was measured, it was below the detection limit (50 ppm by volume). This was combined with a skin material in the same manner as in Example 1, and evaluated using the obtained fiber-reinforced composite. Details of the conditions are shown in Table 1. The fiber reinforced composite of Example 4 had excellent appearance, adhesiveness, and dimensional reproducibility as in Example 2.
- Example 5 A polyphenylene ether resin (PPE) 50 mass% and a polystyrene resin (PS) 50 mass% were heated, melted and kneaded by an extruder and then extruded to prepare a base resin pellet as a core material.
- PPE polyphenylene ether resin
- PS polystyrene resin
- the dimensional change rate at 130 ° C. of the obtained bead foam molded product was a shrinkage of 0.1% or less.
- concentration of the aliphatic hydrocarbon gas in the obtained bead foam molded product was measured, it was below the detection limit (50 ppm by volume).
- This was combined with a skin material in the same manner as in Example 1, and evaluated using the obtained fiber-reinforced composite. Details of the conditions are shown in Table 1.
- the fiber reinforced composite of Example 5 had excellent appearance, adhesiveness, and dimensional reproducibility as in Example 2.
- Example 6 A polyphenylene ether-based resin (PPE) 60 mass% and a polystyrene-based resin (PS) 40 mass% were heated, melted and kneaded by an extruder, and then extruded to produce a base resin pellet as a core material.
- PPE polyphenylene ether-based resin
- PS polystyrene-based resin
- the coefficient of linear expansion of the obtained bead foam molded product was measured to be 2 ⁇ 10 ⁇ 5 mm / mm ⁇ ° C.
- the dimensional change rate at 130 ° C. of the obtained bead foam molded product was a shrinkage of 0.1% or less.
- concentration of the aliphatic hydrocarbon gas in the obtained bead foam molded product was measured, it was below the detection limit (50 ppm by volume).
- This was combined with a skin material in the same manner as in Example 1, and evaluated using the obtained fiber-reinforced composite. Details of the conditions are shown in Table 1.
- the fiber reinforced composite of Example 6 had excellent appearance, adhesiveness, and dimensional reproducibility as in Example 2.
- Example 7 A polyphenylene ether-based resin (PPE) 35 mass% and a polystyrene-based resin (PS) 65 mass% were heated, melted and kneaded by an extruder and then extruded to prepare a base resin pellet as a core material.
- PPE polyphenylene ether-based resin
- PS polystyrene-based resin
- the dimensional change rate at 130 ° C. of the obtained bead foam molded product was a shrinkage of 0.1% or less.
- concentration of the aliphatic hydrocarbon gas in the obtained bead foam molded product was measured, it was below the detection limit (50 ppm by volume).
- This was combined with a skin material in the same manner as in Example 1, and evaluated using the obtained fiber-reinforced composite. Details of the conditions are shown in Table 1.
- the fiber reinforced composite of Example 7 had excellent appearance, adhesiveness, and dimensional reproducibility as in Example 2.
- Example 8 30 mass% of polyphenylene ether resin (PPE) and 70 mass% of polystyrene resin (PS) were heated, melted and kneaded by an extruder, and then extruded to prepare a base resin pellet as a core material.
- PPE polyphenylene ether resin
- PS polystyrene resin
- Tp 150 degreeC
- G'2 / G'1 was 0.28.
- a bead foam molding was produced in the same manner as in Example 1. It was 80 degreeC when the heat shrink start temperature of the obtained bead foam molding was measured.
- the linear expansion coefficient of the obtained bead foam molded product was measured, it was 5 ⁇ 10 ⁇ 5 mm / mm ⁇ ° C.
- the dimensional change rate at 130 ° C. of the obtained bead foam molding was ⁇ 0.3%.
- concentration of the aliphatic hydrocarbon gas in the obtained bead foam molded product was measured, it was below the detection limit (50 ppm by volume).
- This was combined with a skin material in the same manner as in Example 1, and evaluated using the obtained fiber-reinforced composite. Details of the conditions are shown in Table 1. Although the fiber-reinforced composite of Example 8 was slightly wrinkled in appearance, it was at a level where there was no practical problem. Further, the composite was slightly thinner and the apparent density was higher than that of Example 1.
- Example 1 The concentration of the aliphatic hydrocarbon gas in the obtained bead foam molded product was measured, it was below the detection limit (50 ppm by volume). This was combined with the skin material in the same manner as in Example 1. Details of the conditions are shown in Table 1. In Comparative Example 1, the core material was melted at the time of composite, and a fiber-reinforced composite could not be obtained.
- Example 2 a fiber-reinforced composite can be obtained, and although the thickness and the apparent density are good, the appearance of the resin is often withered and wrinkled due to the large linear expansion coefficient. There were many gaps between them, which could not withstand actual use.
- the dimensional change rate at 130 ° C. of the obtained bead foam molding was ⁇ 5.0%.
- concentration of the aliphatic hydrocarbon gas in the obtained bead foam molded product was measured, it was below the detection limit (50 ppm by volume).
- This was combined with a skin material in the same manner as in Example 1, and evaluated using the obtained fiber-reinforced composite. Details of the conditions are shown in Table 1.
- Comparative Example 4 a fiber-reinforced composite could be obtained, but the core material was greatly shrunk and was not a material that could withstand actual use.
- the dimensional change rate at 130 ° C. of the obtained bead foam molding was ⁇ 2.7%.
- concentration of the aliphatic hydrocarbon gas in the obtained bead foam molded product was measured, it was below the detection limit (50 ppm by volume).
- This was combined with a skin material in the same manner as in Example 1, and evaluated using the obtained fiber-reinforced composite. Details of the conditions are shown in Table 1.
- Comparative Example 5 as a result of shrinkage of the molded product, wrinkles were observed on the surface due to the small thickness, high apparent density, and low shrinkage start temperature, and the product was not durable.
- a bead foam molded article was produced in the same manner as in Example 2 except that the foaming gas was pentane. It was 90 degreeC when the heat shrink start temperature of the obtained bead foam molding was measured. When the linear expansion coefficient of the obtained bead foam molded product was measured, it was 5 ⁇ 10 ⁇ 5 mm / mm ⁇ ° C. The dimensional change rate at 130 ° C. of the obtained bead foam molding was + 1.5%. It was 1500 volume ppm when the density
- Comparative Example 6 was slightly inferior to the surface smoothness as compared with Example 2, but the appearance was at a level that could withstand use. However, due to the expansion of the bead foam molding, there were many gaps between the skin material and the core material, and the adhesiveness was not a thing that could withstand actual use. In addition, it was difficult to control the expansion, resulting in poor dimensional reproducibility.
- the core material for a fiber reinforced composite of the present invention is excellent in processability when combined with a fiber reinforced material, and the fiber reinforced composite using the fiber reinforced composite is particularly used in the automobile field (for example, an automobile roof, bonnet, fender, etc.). Member).
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Abstract
Description
ビーズ発泡成形体は、熱可塑性樹脂を含み、任意選択的に、微量のガス、添加剤等を含む。
上記ビーズ発泡成形体中の熱可塑性樹脂の含有量は、50~100質量%であることが好ましく、熱可塑性樹脂のみからなるビーズ発泡成形体であってもよい。
熱可塑性樹脂は、特には限定されないが、70℃~200℃において損失正接tanδが最大となる温度をTpとし、(Tp-30)℃の貯蔵弾性率(G’1)と150℃の貯蔵弾性率(G’2)の比(G’2/G’1)が0.25~0.95であることが好ましい。G’2/G’1がこの範囲にあると、高温での剛性を適度に維持しやすくなり、複合時の変形を抑制しやすく、また、繊維強化材と馴染みやすくなり、接着強度を発現しやすくなる。G’2/G’1は、より好ましくは0.30~0.90、さらに好ましくは0.30~0.85である。
ポリフェニレンエーテル系樹脂は、下記一般式(1)で表される繰り返し単位を含む重合体をいい、例えば、下記一般式(1)で表される繰り返し単位からなる単独重合体、下記一般式(1)で表される繰り返し単位を含む共重合体等が挙げられる。
ポリフェニレンエーテル系樹脂は、1種単独で用いても、2種以上を組み合わせて用いてもよい。
他の樹脂としては、熱可塑性樹脂等が挙げられ、例えば、ポリエチレン、ポリプロピレン、EVA(エチレン-酢酸ビニル共重合体)等のポリオレフィン系樹脂;ポリビニルアルコール;ポリ塩化ビニル;ポリ塩化ビニリデン;ABS(アクリロニトリル-ブタジエン-スチレン)樹脂;AS(アクリロニトリル-スチレン)樹脂;ポリスチレン系樹脂;メタクリル系樹脂;ポリアミド系樹脂;ポリカーボネート系樹脂;ポリイミド系樹脂;ポリアセタール系樹脂;ポリエステル系樹脂;アクリル系樹脂;セルロース系樹脂;スチレン系、ポリ塩化ビニル系、ポリウレタン系、ポリエステル系、ポリアミド系、1,2-ポリブタジエン系、フッ素ゴム系等の熱可塑性エラストマー;ポリアミド系、ポリアセタール系、ポリエステル系、フッ素系の熱可塑性エンジニアリングプラスチック;等が挙げられる。また本発明の目的を損なわない範囲で、変性、架橋された樹脂を用いてもよい。中でも、相溶性の観点から、ポリスチレン系樹脂が好ましい。
これらは、1種単独で用いても、2種以上を組み合わせて用いてもよい。
スチレン誘導体としては、特に限定されないが、例えば、o-メチルスチレン、m-メチルスチレン、p-メチルスチレン、t-ブチルスチレン、α-メチルスチレン、β-メチルスチレン、ジフェニルエチレン、クロロスチレン、ブロモスチレン等が挙げられる。
スチレン又はスチレン誘導体の単独重合体としては、例えば、ポリスチレン、ポリα-メチルスチレン、ポリクロロスチレン等が挙げられる。
スチレン及び/又はスチレン誘導体を主成分とする共重合体としては、例えば、スチレン-α-オレフィン共重合体;スチレン-ブタジエン共重合体;スチレン-アクリロニトリル共重合体;スチレン-マレイン酸共重合体;スチレン-無水マレイン酸共重合体;スチレン-マレイミド共重合体;スチレン-N-フェニルマレイミド共重合体;スチレン-N-アルキルマレイミド共重合体;スチレン-N-アルキル置換フェニルマレイミド共重合体;スチレン-アクリル酸共重合体;スチレン-メタクリル酸共重合体;スチレン-メチルアクリレート共重合体;スチレン-メチルメタクリレート共重合体;スチレン-n-アルキルアクリレート共重合体;スチレン-n-アルキルメタクリレート共重合体;エチルビニルベンゼン-ジビニルベンゼン共重合体;ABS、ブタジエン-アクリロニトリル-α-メチルベンゼン共重合体等の三元共重合体;スチレングラフトポリエチレン、スチレングラフトエチレン-酢酸ビニル共重合体、(スチレン-アクリル酸)グラフトポリエチレン、スチレングラフトポリアミド等のグラフト共重合体;等が挙げられる。
これらは、1種単独で用いても、2種以上を組み合わせて用いてもよい。
ゴム成分の含有量は、ポリスチレン系樹脂100質量%に対して、1.0~20質量%であることが好ましく、3.0~18質量%であることがより好ましい。
ガスとは、ビーズ発泡成形体の製造過程(後述)において含まれることとなるものである。
ガスとしては、特に限定されないが、空気、炭酸ガス、発泡剤として用いられる各種ガス、脂肪族炭化水素系ガス等が挙げられる。
脂肪族炭化水素系ガスとしては、具体的には、ブタン、ペンタン等が挙げられる。
なお、脂肪族炭化水素系ガスの含有量は、ガスクロマトグラフィーにより測定することができる。
脂肪族炭化水素系ガスの含有量を500体積ppm以下とすれば、複合時の加熱によるビーズ発泡成形体の膨張を抑制しやすくなる為、優れた表面平滑性、接着性、強度を得やすくなり、寸法の再現性も良く、後膨れも抑制しやすくなる。また、厚みの異なる箇所がある形状等、より複雑な形状での複合を行いやすくなる。
添加剤としては、例えば、難燃剤、ゴム成分、酸化防止剤、熱安定剤、滑剤、顔料、染料、耐光性改良剤、帯電防止剤、耐衝撃改質剤、タルク等の核剤、ガラスビーズ、無機充填剤、アンチブロッキング剤等が挙げられる。
なお、熱収縮開始温度は、後述の実施例に記載の方法により測定することができる。
なお、線膨張係数は、後述の実施例に記載の方法により測定することができる。
なお、130℃での加熱寸法変化率は、後述の実施例に記載の方法により測定することができる。
なお、発泡倍率は、後述の実施例に記載の方法により測定することができる。
これらは、1種単独で用いてもよく、2種以上併用してもよい。
ガスの安全性の観点から無機ガスが好ましい。また、無機ガスは炭化水素等の有機ガスに比べ樹脂に溶けにくく、発泡工程や成形工程の後、樹脂からガスが抜けやすいので、成形品の経時での寸法安定性がより優れる利点もある。さらに、残存ガスによる樹脂の可塑化も起こりにくく、成形後、より早い段階から優れた耐熱性を発現しやすいメリットもある。無機ガスの中でも、樹脂への溶解性、取り扱いの容易さの観点から、炭酸ガスが好ましく、その含浸量は樹脂に対して0.5~10質量%あることが好ましい。より好ましくは1.0~9質量%である。
なお、発泡ビーズの発泡倍率とは、発泡ビーズの重量Wpに対する、発泡ビーズの体積Vpの割合(Vp/Wp)をいう。また、本明細書において、発泡ビーズの体積は、水没法で測定した体積をいう。
なお、ビーズ発泡成形体の発泡倍率とは、ビーズ発泡成形体の重量Wbに対する、ビーズ発泡成形体の体積Vbの割合(Vb/Wb)をいう。また、本明細書において、ビーズ発泡成形体の体積は、水没法で測定した体積をいう。
本実施形態の芯材を用いて、繊維強化材(例えば、表皮材)と複合し、繊維強化複合体を得ることができる。繊維強化複合体は、ビーズ発泡成形体を含む芯材の表面の少なくとも一部に、繊維及び樹脂を含む表皮材が配置された複合体である。芯材は、ビーズ発泡成形体のみからなる芯材であってもよい。
本実施形態の繊維強化複合体における表皮材は、繊維及び樹脂を含み、任意選択的に、添加剤等を含む。
繊維としては、高強度、高弾性率の繊維が挙げられ、具体的には、炭素繊維、ガラス繊維、有機繊維(例えば、米国デュポン(株)社製の「ケブラー(登録商標)」に代表されるポリアラミド繊維)、アルミナ繊維、シリコンカーバイド繊維、ボロン繊維、炭化ケイ素繊維等が挙げられる。
これら繊維は、1種単独で用いてもよく、2種以上を併用してもよい。
樹脂としては、熱硬化性樹脂や熱可塑性樹脂が挙げられ、エポキシ樹脂、フェノール樹脂、シアネート樹脂、ベンゾオキサジン樹脂、ポリイミド樹脂、不飽和ポリエステル樹脂、ビニルエステル樹脂、ABS樹脂、ポリエチレンテレフタレート樹脂、ナイロン樹脂、マレイミド樹脂等が挙げられる。
これら樹脂は、1種単独で用いてもよく、2種以上を併用してもよい。
なお、ガラス転移温度は、ASTM-D-3418に準拠して中点法により測定することができる。
本実施形態における樹脂の含有量は、芯材との接着性、変形や反りの観点から、表皮材100質量%に対して、20~60質量%であることが好ましく、より好ましくは、30~50質量%である。
以下、本実施形態の繊維強化複合体の製造方法について記載する。
本実施形態における一例の繊維強化複合体の製造方法は、ビーズ発泡成形体を含む芯材と、繊維と樹脂とを含む表皮材とを、成形機内に加えて成形を行うことによって、繊維強化複合体を得る方法である。尚、芯材の形状は、特に限定されることなく、目的や用途に応じて適宜定めることができ、例えば、成形品、粒子状、シート状、線状(糸状)、塊状等が挙げられる。
表皮材調製工程では、溶融状態の樹脂中に繊維を浸漬させたり、溶融状態の樹脂を繊維に吹き付けたりして、樹脂に繊維を含浸させて、表皮材を得る。表皮材は、クロスプリプレグとして調製してよい。
なお、樹脂に繊維を含浸させた後に、光や熱により樹脂の硬化を進ませておいてもよい。
繊維強化複合体の形状もシート状である場合には、本実施形態の繊維強化複合体について記載した通りとしてもよい。
成形工程では、芯材(例えば、ビーズ発泡成形体)と表皮材とを、所望の配置状態で、成形機内に充填して、同時に成形を行ってよい。
なお、ビーズ発泡成形体は、成形工程においてさらに発泡されてよい。
このように、加圧前に、圧力をかけずに高温条件下で保持することによって、表皮材に均一に熱を加えて、表面平滑性を得ることができる。
なお、繊維強化複合体の見かけ密度とは、繊維強化複合体の体積Vに対する、繊維強化複合体の重量の割合(W/V)をいう。
表皮材の厚さとしては、概して、0.1~2mmとしてよい。
300mm×100mm×厚み10mmの平板状のビーズ発泡成形体を23℃に調整した環境に24時間静置した。このビーズ発泡成形体に200mmの直線を20mm間隔で平行に三本引き、ノギスで線の長さ(mm)を測定した。その後、30℃のオーブンにビーズ発泡成形体を2時間投入後、23℃で1時間静置した後の線の長さ(mm)を測定した。この測定を、5℃刻みにオーブンの温度を上げて繰り返し、23℃で測定した線の長さを三本全て下回ったときの温度を熱収縮開始温度(℃)とした。
300mm×100mm×厚み10mmの平板状のビーズ発泡成形体を23℃に調整した環境に24時間静置した。このビーズ発泡成形体に200mmの直線を20mm間隔で平行に三本引き、ノギスで線の長さ(mm)を測定した(寸法A)。40℃に調整した環境にビーズ発泡成形体を2時間投入後、取り出した直後の線の長さ(mm)を測定した(寸法B)。同じビーズ発泡成形体を5℃に調整した環境に2時間投入後、取り出した直後の線の長さ(mm)を測定した(寸法C)。それぞれの線について、下記式にて線膨張係数を計算し、その平均値をビーズ発泡成形体の線膨張係数(mm/mm・℃)とした。
線膨張係数=(寸法B-寸法C)/(寸法A×35)
加熱温度を130℃、加熱時間を1.5分とする以外は、JIS K6767の高温時の寸法安定性試験B法に準じて測定を行った。なお、加熱時間は、熱風循環式乾燥機内に試験片を投入後、乾燥機内温度が130℃に到達してから1.5分とした。
発泡前の樹脂について、TAインスツルメント社製ARES-G2を用いて、下記条件にて粘弾性測定を行った。尚、測定は300℃から降温しながら行うが、途中で樹脂が固化して測定不能となった場合は、その温度までのデータを用いることとした。得られたデータから、70℃(途中で測定不能となった場合はその温度)~200℃において損失正接tanδが最大となる温度をTpとし、(Tp-30)℃及び150℃の貯蔵弾性率、それぞれG’1及びG’2を求め、G’2/G’1を計算した。なお、途中で測定不能となり、(Tp-30℃)のデータが得られなかった場合は、測定不能となった温度の貯蔵弾性率をG’1とする。
測定治具 :コーン&プレート
測定モード :溶融
掃引カテゴリー:温度掃引
歪み量 :10%
周波数 :10rad/sec
温度範囲 :70~300℃
降温速度 :2℃/min
プレート径 :25φmm
ギャップ間隔 :1mm
自動モード :Axial force…10g
Sensitivity…2.0g
実施例及び比較例で得られたビーズ発泡成形体を試料として適量ヘッドスペースボトルに仕込み、ビーズ発泡成形体試料の軟化点以上の温度で約1時間加熱した。その後、ガスクロマトグラフィー(島津製作所製、GC14B)により、ヘッドスペースボトル内のガスを定量した。キャリアガスとしてヘリウム(He)を用い、定流量モード(約30mL/分)で制御した。また、カラム(Porapak Q、80/100mesh、3.2mmφ×2.1m)を50~150℃で昇温、保持を行い、熱伝導度型検出器(TCD)により検出を行った。検出したエリア面積と標準ガス試料で作成した検量線とから、脂肪族炭化水素系ガスの体積を算出した。そして、脂肪族炭化水素系ガスの体積をビーズ発泡成形体試料の体積で除して、脂肪族炭化水素系ガスの濃度(体積ppm)を算出した。
ビーズ発泡成形体の重量W(g)を測定した後、水没法で体積V(cc)を測定し、その体積を重量で除した値V/W(cc/g)を発泡倍率(cm3/g)とした。
実施例及び比較例で得られた繊維強化複合体の厚み(mm)及び表皮材の厚み(mm)をノギスを用いて測定した。
実施例及び比較例で得られた繊維強化複合体の重量W(g)を測定した後、ノギスにてシート状の繊維強化複合体の3辺を測定し、その体積V(cm3)を計算した。そして、体積Vに対する重量Wの割合(W/V)(g/cm3)を見かけ密度とした。
実施例及び比較例で得られたビーズ発泡成形体を用いて表皮材と複合し、繊維強化複合体の表面を目視にて観察し、以下のように評価した。
◎(優れる):しわや気泡がなく、表面平滑性が良好なもの。
○(良好):しわや気泡が若干発生するが、実使用上は問題のないもの。
×(劣る):樹脂枯れもしくは、しわが多く実使用が不可なもの。
実施例及び比較例で得られたビーズ発泡成形体を用いて表皮材と複合し、繊維強化複合体の中心部及び端から10mmの箇所で切断し、その断面を目視にて観察し、表皮材と芯材との接着状態を以下のように評価した。
◎(優れる):表皮材と芯材との間に隙間はなく、接着性が良好なもの。
○(良好):表皮材と芯材との間に一部隙間があるが、実使用上は問題のないもの。
×(劣る):表皮材と芯材の間の隙間や剥離が多く、実使用が不可なもの。
実施例及び比較例で得られたビーズ発泡成形体を用いて表皮材と複合し、繊維強化複合体30個について、それぞれ縦・横の長さをノギスを用いて測定し、測定値の3σ及び平均値を計算し、(3σ/平均値)×100をばらつき(%)とした。
◎(優れる):ばらつきが0.3%以下のもの
○(良好):ばらつきが0.3~0.5%のもの
×(劣る):ばらつきが0.5%より大きいもの
引張弾性率が250GPaの炭素繊維と硬化温度が80℃であるエポキシ樹脂とで構成される、繊維の目付量が200g/m2、炭素繊維含有量が60質量%のクロスプリプレグを、表皮材として2枚用意した。
また、ポリフェニレンエーテル系樹脂(PPE)を73質量%、ゴム濃度が6質量%の耐衝撃性ポリスチレン樹脂(HIPS)を12質量%(基材樹脂中のゴム成分含有量は0.6質量%)、汎用ポリスチレン樹脂(PS)を15質量%用い、これら熱可塑性樹脂100質量%に対し、非ハロゲン系難燃剤を22質量%添加し、押出機にて加熱溶融混練した後に押し出し、芯材としての基材樹脂ペレットを作製した。この基材樹脂の粘弾性測定を実施したところ、Tpは153℃、G’2/G’1は0.40であった。
特開平4-372630号公報の実施例1に記載の方法に準じ、基材樹脂ペレットを耐圧容器に収容し、容器内の気体を乾燥空気で置換した後、発泡剤として二酸化炭素(気体)を注入し、圧力3.2MPa、温度11℃の条件下で3時間かけて、基材樹脂ペレットに対して二酸化炭素を7質量%含浸させた。
その後、基材樹脂ペレットを予備発泡機内で攪拌羽を77rpmにて回転させながら、加圧水蒸気により発泡させて、発泡ビーズを得た。
この発泡ビーズを0.5MPaまで1時間かけて昇圧し、その後0.5MPaで8時間保持し、加圧処理を施した。
これを、水蒸気孔を有する型内成形金型内に充填し、加圧水蒸気で加熱して発泡ビーズ相互を膨張・融着させた後、冷却し、成形金型より取り出し、300mm×300mm×10mm厚み、発泡倍率10cm3/gのビーズ発泡成形体(発泡体)を得た。
得られたビーズ発泡成形体の熱収縮開始温度を測定すると85℃であった。得られたビーズ発泡成形体の線膨張係数を測定すると、5×10-5mm/mm・℃であった。得られたビーズ発泡成形体の130℃での寸法変化率は-3.6%であった。得られたビーズ発泡成形体の脂肪族炭化水素系ガスの濃度を測定したところ、検出限界(50体積ppm)以下であった。
得られたビーズ発泡成形体を芯材として用い、上述の通り用意した表皮材を芯材の上下両面に1枚ずつ積層し、次いで、この積層体を、圧力をかけずに、100℃で3分間保持した後、面圧0.4MPaで加圧しながら、15分間保持することによって、表皮材と芯材とを同時成形して繊維強化複合体を得た。
諸条件の詳細を表1に示す。
実施例1の繊維強化複合体の外観は、しわや気泡がなく、優れたものであった。接着性は、表皮材と芯材との間に一部隙間があるが、実使用上は問題のないレベルであった。また、寸法再現性も若干寸法変動はあるものの、実使用上は問題のないレベルであった。
ポリフェニレンエーテル系樹脂(PPE)40質量%、ポリスチレン系樹脂(PS)60質量%を、押出機にて加熱溶融混練した後に押出し、芯材としての基材樹脂ペレットを作製した。この基材樹脂の粘弾性測定を実施したところ、Tpは158℃、G’2/G’1は0.81であった。
これを用い実施例1と同様にビーズ発泡成形体を作製した。
得られたビーズ発泡成形体の熱収縮開始温度を測定すると95℃であった。得られたビーズ発泡成形体の線膨張係数を測定すると、4×10-5mm/mm・℃であった。得られたビーズ発泡成形体の130℃での寸法変化率は0.1%以下の収縮であった。得られたビーズ発泡成形体の脂肪族炭化水素系ガスの濃度を測定したところ、検出限界(50体積ppm)以下であった。
これを実施例1と同様に表皮材と複合し、得られた繊維強化複合体を用いて評価を行った。
諸条件の詳細を表1に示す。
実施例2の繊維強化複合体は、外観、接着性、寸法再現性共に優れていた。
実施例2の熱可塑性樹脂を用い、発泡倍率5cm3/gのビーズ発泡成形体を作製した。
得られたビーズ発泡成形体の熱収縮開始温度を測定すると95℃であった。得られたビーズ発泡成形体の線膨張係数を測定すると、4×10-5mm/mm・℃であった。得られたビーズ発泡成形体の130℃での寸法変化率は0.1%以下の収縮であった。得られたビーズ発泡成形体の脂肪族炭化水素系ガスの濃度を測定したところ、検出限界(50体積ppm)以下であった。
これを実施例1と同様に表皮材と複合し、得られた繊維強化複合体を用いて評価を行った。
諸条件の詳細を表1に示す。
実施例3の繊維強化複合体は、実施例2同様に優れた外観、接着性、寸法再現性を有した。
実施例2の熱可塑性樹脂を用い、発泡倍率15cm3/gのビーズ発泡成形体を作製した。
得られたビーズ発泡成形体の熱収縮開始温度を測定すると95℃であった。得られたビーズ発泡成形体の線膨張係数を測定すると、4×10-5mm/mm・℃であった。得られたビーズ発泡成形体の130℃での寸法変化率は0.1%以下の収縮であった。得られたビーズ発泡成形体の脂肪族炭化水素系ガスの濃度を測定したところ、検出限界(50体積ppm)以下であった。
これを実施例1と同様に表皮材と複合し、得られた繊維強化複合体を用いて評価を行った。
諸条件の詳細を表1に示す。
実施例4の繊維強化複合体は、実施例2同様に優れた外観、接着性、寸法再現性を有した。
ポリフェニレンエーテル系樹脂(PPE)50質量%、ポリスチレン系樹脂(PS)50質量%を、押出機にて加熱溶融混練した後に押出し、芯材としての基材樹脂ペレットを作製した。この基材樹脂の粘弾性測定を実施したところ、Tpは165℃、G’2/G’1は0.87であった。
これを用い実施例1と同様にビーズ発泡成形体を作製した。得られたビーズ発泡成形体の熱収縮開始温度を測定すると105℃であった。得られたビーズ発泡成形体の線膨張係数を測定すると、3×10-5mm/mm・℃であった。得られたビーズ発泡成形体の130℃での寸法変化率は0.1%以下の収縮であった。得られたビーズ発泡成形体の脂肪族炭化水素系ガスの濃度を測定したところ、検出限界(50体積ppm)以下であった。
これを実施例1と同様に表皮材と複合し、得られた繊維強化複合体を用いて評価を行った。
諸条件の詳細を表1に示す。
実施例5の繊維強化複合体は、実施例2同様に優れた外観、接着性、寸法再現性を有した。
ポリフェニレンエーテル系樹脂(PPE)60質量%、ポリスチレン系樹脂(PS)40質量%を、押出機にて加熱溶融混練した後に押出し、芯材としての基材樹脂ペレットを作製した。この基材樹脂の粘弾性測定を実施したところ、Tpは173℃、G’2/G’1は0.93であった。
これを用い実施例1と同様にビーズ発泡成形体を作製した。得られたビーズ発泡成形体の熱収縮開始温度を測定すると115℃であった。得られたビーズ発泡成形体の線膨張係数を測定すると、2×10-5mm/mm・℃であった。得られたビーズ発泡成形体の130℃での寸法変化率は0.1%以下の収縮であった。得られたビーズ発泡成形体の脂肪族炭化水素系ガスの濃度を測定したところ、検出限界(50体積ppm)以下であった。
これを実施例1と同様に表皮材と複合し、得られた繊維強化複合体を用いて評価を行った。
諸条件の詳細を表1に示す。
実施例6の繊維強化複合体は、実施例2同様に優れた外観、接着性、寸法再現性を有した。
ポリフェニレンエーテル系樹脂(PPE)35質量%、ポリスチレン系樹脂(PS)65質量%を、押出機にて加熱溶融混練した後に押出し、芯材としての基材樹脂ペレットを作製した。この基材樹脂の粘弾性測定を実施したところ、Tpは154℃、G’2/G’1は0.45であった。
これを用い実施例1と同様にビーズ発泡成形体を作製した。得られたビーズ発泡成形体の熱収縮開始温度を測定すると85℃であった。得られたビーズ発泡成形体の線膨張係数を測定すると、5×10-5mm/mm・℃であった。得られたビーズ発泡成形体の130℃での寸法変化率は0.1%以下の収縮であった。得られたビーズ発泡成形体の脂肪族炭化水素系ガスの濃度を測定したところ、検出限界(50体積ppm)以下であった。
これを実施例1と同様に表皮材と複合し、得られた繊維強化複合体を用いて評価を行った。
諸条件の詳細を表1に示す。
実施例7の繊維強化複合体は、実施例2同様に優れた外観、接着性、寸法再現性を有した。
ポリフェニレンエーテル系樹脂(PPE)30質量%、ポリスチレン系樹脂(PS)70質量%を、押出機にて加熱溶融混練した後に押出し、芯材としての基材樹脂ペレットを作製した。この基材樹脂の粘弾性測定を実施したところ、Tpは150℃、G’2/G’1は0.28であった。
これを用い実施例1と同様にビーズ発泡成形体を作製した。得られたビーズ発泡成形体の熱収縮開始温度を測定すると80℃であった。得られたビーズ発泡成形体の線膨張係数を測定すると、5×10-5mm/mm・℃であった。得られたビーズ発泡成形体の130℃での寸法変化率は-0.3%であった。得られたビーズ発泡成形体の脂肪族炭化水素系ガスの濃度を測定したところ、検出限界(50体積ppm)以下であった。
これを実施例1と同様に表皮材と複合し、得られた繊維強化複合体を用いて評価を行った。
諸条件の詳細を表1に示す。
実施例8の繊維強化複合体は、外観に若干しわが発生したものの、実用上の問題は無いレベルであった。また、若干複合体の厚みが薄く、見かけ密度も実施例1に比べて高くなる結果になった。
ポリスチレン系樹脂(PS)100質量%を押出機にて加熱溶融混練した後に押出し、芯材としての基材樹脂ペレットを作製した。この基材樹脂の粘弾性測定を実施したところ、Tpは118℃、G’2/G’1は0.01以下であった。
これを用い実施例1と同様にビーズ発泡成形体を作製した。得られたビーズ発泡成形体の熱収縮開始温度を測定すると70℃であった。得られたビーズ発泡成形体の線膨張係数を測定すると、7×10-5mm/mm・℃であった。得られたビーズ発泡成形体の130℃での寸法変化率は-20%であった。得られたビーズ発泡成形体の脂肪族炭化水素系ガスの濃度を測定したところ、検出限界(50体積ppm)以下であった。
これを実施例1と同様に表皮材と複合した。
諸条件の詳細を表1に示す。
比較例1は、複合時に芯材が溶融し、繊維強化複合体を得ることができなかった。
ポリプロピレン系樹脂(PP)100質量%を押出機にて加熱溶融混練した後に押出し、芯材としての基材樹脂ペレットを作製した。この基材樹脂の粘弾性測定を実施したところ、Tpは153℃、G’2/G’1は0.14であった。
これを用い実施例1と同様にビーズ発泡成形体を作製した。得られたビーズ発泡成形体の熱収縮開始温度を測定すると95℃であった。得られたビーズ発泡成形体の線膨張係数を測定すると、12×10-5mm/mm・℃であった。得られたビーズ発泡成形体の130℃での寸法変化率は-0.5%であった。得られたビーズ発泡成形体の脂肪族炭化水素系ガスの濃度を測定したところ、検出限界(50体積ppm)以下であった。
これを実施例1と同様に表皮材と複合し、得られた繊維強化複合体を用いて評価を行った。
諸条件の詳細を表1に示す。
比較例2は繊維強化複合体を得ることができ、厚みや見かけ密度は良好なものの、線膨張係数が大きい影響で外観に樹脂枯れやしわが多く見られ、またその影響で表皮材と芯材の間の隙間も多発しており、実使用には耐えないものであった。
ポリメチルメタクリレート系樹脂(PMMA)100質量%を押出機にて加熱溶融混練した後に押出し、ミニペレットを作成した。この基材樹脂の粘弾性測定を実施したところ、Tpは127℃、G’2/G’1は0.01以下であった。
これを用い実施例1と同様にビーズ発泡成形体を作製した。得られたビーズ発泡成形体の熱収縮開始温度を測定すると75℃であった。得られたビーズ発泡成形体の線膨張係数を測定すると、8×10-5mm/mm・℃であった。得られたビーズ発泡成形体の130℃での寸法変化率は-15%であった。得られたビーズ発泡成形体の脂肪族炭化水素系ガスの濃度を測定したところ、検出限界(50体積ppm)以下であった。
これを実施例1と同様に表皮材と複合した。
諸条件の詳細を表1に示す。
比較例3は、比較例1と同様に芯材が溶融し、複合体を得ることができなかった。
ポリスチレン系樹脂(スチレン-メタクリル酸共重合体)(SMAA)100質量%を押出機にて加熱溶融混練した後に押出し、ミニペレットを作成した。この基材樹脂の粘弾性測定を実施したところ、Tpは145℃、G’2/G’1は0.17であった。
これを用い実施例1と同様にビーズ発泡成形体を作製した。得られたビーズ発泡成形体の熱収縮開始温度を測定すると80℃であった。得られたビーズ発泡成形体の線膨張係数を測定すると、7×10-5mm/mm・℃であった。得られたビーズ発泡成形体の130℃での寸法変化率は-5.0%であった。得られたビーズ発泡成形体の脂肪族炭化水素系ガスの濃度を測定したところ、検出限界(50体積ppm)以下であった。
これを実施例1と同様に表皮材と複合し、得られた繊維強化複合体を用いて評価を行った。
諸条件の詳細を表1に示す。
比較例4は繊維強化複合体を得ることができたが、芯材の収縮が大きく、実使用に耐える物ではなかった。
ポリフェニレンエーテル系樹脂(PPE)20質量%、ポリスチレン系樹脂(PS)80質量%を、押出機にて加熱溶融混練した後に押出し、芯材としての基材樹脂ペレットを作製した。この基材樹脂の粘弾性測定を実施したところ、Tpは141℃、G’2/G’1は0.04であった。
これを用い実施例1と同様にビーズ発泡成形体を作製した。得られたビーズ発泡成形体の熱収縮開始温度を測定すると75℃であった。得られたビーズ発泡成形体の線膨張係数を測定すると、6×10-5mm/mm・℃であった。得られたビーズ発泡成形体の130℃での寸法変化率は-2.7%であった。得られたビーズ発泡成形体の脂肪族炭化水素系ガスの濃度を測定したところ、検出限界(50体積ppm)以下であった。
これを実施例1と同様に表皮材と複合し、得られた繊維強化複合体を用いて評価を行った。
諸条件の詳細を表1に示す。
比較例5は、成形品が収縮した結果、厚みが薄く、見かけ密度が高く、更に収縮開始温度が低い影響で、表面にしわが観察され、実使用に耐えないものであった。
発泡ガスをペンタンとする以外は実施例2と同様にビーズ発泡成形体を作製した。
得られたビーズ発泡成形体の熱収縮開始温度を測定すると90℃であった。得られたビーズ発泡成形体の線膨張係数を測定すると、5×10-5mm/mm・℃であった。得られたビーズ発泡成形体の130℃での寸法変化率は+1.5%であった。得られたビーズ発泡成形体の脂肪族炭化水素系ガスの濃度を測定したところ、1500体積ppmであった。
これを実施例1と同様に表皮材と複合し、得られた繊維強化複合体を用いて評価を行った。
諸条件の詳細を表1に示す。
比較例6は、実施例2に比べ若干表面平滑性に劣るが、外観は使用に耐えるレベルであった。しかし、ビーズ発泡成形体の膨張の影響で、表皮材と芯材の間の隙間が多く、接着性は実使用に耐える物ではなかった。また、膨張の制御が難しい影響で、寸法再現性も劣る物となった。
Claims (6)
- 熱可塑性樹脂を含み、熱収縮開始温度が80℃以上であり、線膨張係数が10×10-5mm/mm・℃以下であり、130℃での加熱寸法変化率が-4.0~0%であるビーズ発泡成形体を含むことを特徴とする繊維強化複合体用芯材。
- 前記熱可塑性樹脂が、70℃~200℃において損失正接tanδが最大となる温度をTpとし、(Tp-30)℃の貯蔵弾性率(G’1)と150℃の貯蔵弾性率(G’2)の比(G’2/G’1)が0.25~0.95である、請求項1に記載の繊維強化複合体用芯材。
- 前記ビーズ発泡成形体中の脂肪族炭化水素系ガスの濃度が500体積ppm以下である、請求項1又は2に記載の繊維強化複合体用芯材。
- 前記熱可塑性樹脂が、ポリフェニレンエーテル系樹脂を30~75質量%含む、請求項1~3のいずれか1項に記載の繊維強化複合体用芯材。
- 前記熱可塑性樹脂中の難燃剤の含有量が、前記熱可塑性樹脂100質量%に対して3質量%以下である、請求項1~4のいずれか1項に記載の繊維強化複合体用芯材。
- 請求項1~5のいずれか1項に記載の繊維強化複合体用芯材の表面の少なくとも一部に、繊維及び樹脂を含む表皮材が配置されたことを特徴とする、繊維強化複合体。
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JP7084459B2 (ja) | 2022-06-14 |
US11034814B2 (en) | 2021-06-15 |
JPWO2018186360A1 (ja) | 2019-11-07 |
KR102281962B1 (ko) | 2021-07-26 |
TWI670170B (zh) | 2019-09-01 |
SG11201909355WA (en) | 2019-11-28 |
CN110461924B (zh) | 2022-03-08 |
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