US20200384704A1 - Continuous-Fiber-Reinforced Resin Molding and Method for Manufacturing Same - Google Patents

Continuous-Fiber-Reinforced Resin Molding and Method for Manufacturing Same Download PDF

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US20200384704A1
US20200384704A1 US16/970,904 US201916970904A US2020384704A1 US 20200384704 A1 US20200384704 A1 US 20200384704A1 US 201916970904 A US201916970904 A US 201916970904A US 2020384704 A1 US2020384704 A1 US 2020384704A1
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Prior art keywords
resin
continuous
fiber
reinforcing fibers
continuous reinforcing
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Yusuke Aratani
Tsutomu Akiyama
Toru Koizumi
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Asahi Kasei Corp
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Asahi Kasei Corp
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Assigned to ASAHI KASEI KABUSHIKI KAISHA reassignment ASAHI KASEI KABUSHIKI KAISHA ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: AKIYAMA, TSUTOMU, KOIZUMI, TORU, ARATANI, Yusuke
Publication of US20200384704A1 publication Critical patent/US20200384704A1/en
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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
    • C08J5/00—Manufacture of articles or shaped materials containing macromolecular substances
    • C08J5/04—Reinforcing macromolecular compounds with loose or coherent fibrous material
    • C08J5/0405—Reinforcing macromolecular compounds with loose or coherent fibrous material with inorganic fibres
    • C08J5/043—Reinforcing macromolecular compounds with loose or coherent fibrous material with inorganic fibres with glass fibres
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
    • B29C43/00—Compression moulding, i.e. applying external pressure to flow the moulding material; Apparatus therefor
    • B29C43/003—Compression moulding, i.e. applying external pressure to flow the moulding material; Apparatus therefor characterised by the choice of material
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
    • B29C70/00—Shaping composites, i.e. plastics material comprising reinforcements, fillers or preformed parts, e.g. inserts
    • B29C70/04—Shaping composites, i.e. plastics material comprising reinforcements, fillers or preformed parts, e.g. inserts comprising reinforcements only, e.g. self-reinforcing plastics
    • B29C70/06—Fibrous reinforcements only
    • B29C70/10—Fibrous reinforcements only characterised by the structure of fibrous reinforcements, e.g. hollow fibres
    • B29C70/16—Fibrous reinforcements only characterised by the structure of fibrous reinforcements, e.g. hollow fibres using fibres of substantial or continuous length
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
    • B29C70/00—Shaping composites, i.e. plastics material comprising reinforcements, fillers or preformed parts, e.g. inserts
    • B29C70/04—Shaping composites, i.e. plastics material comprising reinforcements, fillers or preformed parts, e.g. inserts comprising reinforcements only, e.g. self-reinforcing plastics
    • B29C70/28—Shaping operations therefor
    • B29C70/40—Shaping or impregnating by compression not applied
    • B29C70/42—Shaping or impregnating by compression not applied for producing articles of definite length, i.e. discrete articles
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
    • C08J5/00—Manufacture of articles or shaped materials containing macromolecular substances
    • C08J5/04—Reinforcing macromolecular compounds with loose or coherent fibrous material
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
    • C08J5/00—Manufacture of articles or shaped materials containing macromolecular substances
    • C08J5/04—Reinforcing macromolecular compounds with loose or coherent fibrous material
    • C08J5/0405—Reinforcing macromolecular compounds with loose or coherent fibrous material with inorganic fibres
    • C08J5/042—Reinforcing macromolecular compounds with loose or coherent fibrous material with inorganic fibres with carbon fibres
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
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    • C08J5/04—Reinforcing macromolecular compounds with loose or coherent fibrous material
    • C08J5/06—Reinforcing macromolecular compounds with loose or coherent fibrous material using pretreated fibrous materials
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
    • C08J5/00—Manufacture of articles or shaped materials containing macromolecular substances
    • C08J5/04—Reinforcing macromolecular compounds with loose or coherent fibrous material
    • C08J5/06—Reinforcing macromolecular compounds with loose or coherent fibrous material using pretreated fibrous materials
    • C08J5/08—Reinforcing macromolecular compounds with loose or coherent fibrous material using pretreated fibrous materials glass fibres
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
    • C08J5/00—Manufacture of articles or shaped materials containing macromolecular substances
    • C08J5/24—Impregnating materials with prepolymers which can be polymerised in situ, e.g. manufacture of prepregs
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29C—SHAPING OR JOINING OF PLASTICS; SHAPING OF MATERIAL IN A PLASTIC STATE, NOT OTHERWISE PROVIDED FOR; AFTER-TREATMENT OF THE SHAPED PRODUCTS, e.g. REPAIRING
    • B29C43/00—Compression moulding, i.e. applying external pressure to flow the moulding material; Apparatus therefor
    • B29C43/32—Component parts, details or accessories; Auxiliary operations
    • B29C43/52—Heating or cooling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29K—INDEXING SCHEME ASSOCIATED WITH SUBCLASSES B29B, B29C OR B29D, RELATING TO MOULDING MATERIALS OR TO MATERIALS FOR MOULDS, REINFORCEMENTS, FILLERS OR PREFORMED PARTS, e.g. INSERTS
    • B29K2077/00—Use of PA, i.e. polyamides, e.g. polyesteramides or derivatives thereof, as moulding material
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29K—INDEXING SCHEME ASSOCIATED WITH SUBCLASSES B29B, B29C OR B29D, RELATING TO MOULDING MATERIALS OR TO MATERIALS FOR MOULDS, REINFORCEMENTS, FILLERS OR PREFORMED PARTS, e.g. INSERTS
    • B29K2101/00—Use of unspecified macromolecular compounds as moulding material
    • B29K2101/12—Thermoplastic materials
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29K—INDEXING SCHEME ASSOCIATED WITH SUBCLASSES B29B, B29C OR B29D, RELATING TO MOULDING MATERIALS OR TO MATERIALS FOR MOULDS, REINFORCEMENTS, FILLERS OR PREFORMED PARTS, e.g. INSERTS
    • B29K2105/00—Condition, form or state of moulded material or of the material to be shaped
    • B29K2105/0005—Condition, form or state of moulded material or of the material to be shaped containing compounding ingredients
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29K—INDEXING SCHEME ASSOCIATED WITH SUBCLASSES B29B, B29C OR B29D, RELATING TO MOULDING MATERIALS OR TO MATERIALS FOR MOULDS, REINFORCEMENTS, FILLERS OR PREFORMED PARTS, e.g. INSERTS
    • B29K2105/00—Condition, form or state of moulded material or of the material to be shaped
    • B29K2105/06—Condition, form or state of moulded material or of the material to be shaped containing reinforcements, fillers or inserts
    • B29K2105/08—Condition, form or state of moulded material or of the material to be shaped containing reinforcements, fillers or inserts of continuous length, e.g. cords, rovings, mats, fabrics, strands or yarns
    • B29K2105/0872—Prepregs
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29K—INDEXING SCHEME ASSOCIATED WITH SUBCLASSES B29B, B29C OR B29D, RELATING TO MOULDING MATERIALS OR TO MATERIALS FOR MOULDS, REINFORCEMENTS, FILLERS OR PREFORMED PARTS, e.g. INSERTS
    • B29K2309/00—Use of inorganic materials not provided for in groups B29K2303/00 - B29K2307/00, as reinforcement
    • B29K2309/08—Glass
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B29—WORKING OF PLASTICS; WORKING OF SUBSTANCES IN A PLASTIC STATE IN GENERAL
    • B29L—INDEXING SCHEME ASSOCIATED WITH SUBCLASS B29C, RELATING TO PARTICULAR ARTICLES
    • B29L2031/00—Other particular articles
    • B29L2031/34—Electrical apparatus, e.g. sparking plugs or parts thereof
    • B29L2031/3481—Housings or casings incorporating or embedding electric or electronic elements
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
    • C08J2363/00—Characterised by the use of epoxy resins; Derivatives of epoxy resins
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
    • C08J2377/00—Characterised by the use of polyamides obtained by reactions forming a carboxylic amide link in the main chain; Derivatives of such polymers
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
    • C08J2377/00—Characterised by the use of polyamides obtained by reactions forming a carboxylic amide link in the main chain; Derivatives of such polymers
    • C08J2377/06—Polyamides derived from polyamines and polycarboxylic acids
    • 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
    • C08J2423/00—Characterised by the use of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Derivatives of such polymers
    • C08J2423/02—Characterised by the use of homopolymers or copolymers of unsaturated aliphatic hydrocarbons having only one carbon-to-carbon double bond; Derivatives of such polymers not modified by chemical after treatment
    • C08J2423/04—Homopolymers or copolymers of ethene
    • C08J2423/06—Polyethene
    • 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
    • C08J2477/00—Characterised by the use of polyamides obtained by reactions forming a carboxylic amide link in the main chain; Derivatives of such polymers
    • C—CHEMISTRY; METALLURGY
    • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
    • C08K—Use of inorganic or non-macromolecular organic substances as compounding ingredients
    • C08K7/00—Use of ingredients characterised by shape
    • C08K7/02—Fibres or whiskers
    • C08K7/04—Fibres or whiskers inorganic
    • C08K7/14—Glass

Definitions

  • the present invention relates to a continuous fiber-reinforced molded resin and to a method for its production. More specifically, the invention relates to a continuous fiber-reinforced molded resin having high adhesive force and affinity at the interface between the continuous reinforcing fibers and the synthetic resin, having small voids in the interface and exhibiting adequate strength, to a continuous fiber-reinforced molded resin with a sufficiently small loss tangent of the continuous fiber-reinforced molded resin and capable of exhibiting sufficient shock absorption, to a continuous fiber-reinforced molded resin with a sufficiently large storage modulus of the continuous fiber-reinforced molded resin and capable of exhibiting sufficient impact strength, and to a continuous fiber-reinforced molded resin having a high resin impregnating property and high strength and rigidity, as well as to a method for producing the same.
  • Molded composite materials having a reinforcing material such as glass fibers added to a matrix resin material have been used in structural parts of various machines and vehicles, or in pressure vessels or tubular structures.
  • a reinforcing material such as glass fibers added to a matrix resin material
  • the reinforcing fibers it is preferred for the reinforcing fibers to be continuous fibers from the viewpoint of strength, and for the resin to be a thermoplastic resin from the viewpoint of the molding cycle and recycling properties.
  • the continuous fiber-reinforced molded resins that have previously been proposed include those with a modified sizing agent added to reinforcing fibers (see PTL 1, for example), those with a modified difference between the melting temperature (melting point) and crystallization temperature of the thermoplastic resin (see PTL 2, for example), those with an organic salt added to a resin material (see PTL 3, for example), those with a molding precursor fabric layered with a thermoplastic resin (see PTL 4, for example), those with reinforcing fibers pre-impregnated with a low-melting-point thermoplastic resin to increase the impregnating property (see PTL 5, for example), and those using two or more resins with different melting points as the surface resins to impart satisfactory resistance against interlayer separation (see PTL 6, for example).
  • continuous fiber-reinforced molded resins of the prior art all have low adhesive force and affinity at the boundaries between the continuous reinforcing fibers, such as glass fibers, and the matrix resin, and consequently have many voids and fail to exhibit sufficient strength in the interface regions between the fibers and resin, so that they do not exhibit the performance required for use in locations where high strength is necessary.
  • continuous fiber-reinforced molded resins of the prior art all have high loss tangents and therefore fail to exhibit sufficient shock absorption and lack performance required for use in locations where high shock absorption is necessary, that they have low storage moduli and thus fail to exhibit sufficient impact strength and lack performance required for use in locations where high impact strength is necessary, and also that the property of resin impregnation into the continuous reinforcing fibers is low, the adhesion between the resin and continuous reinforcing fibers is inadequate, and the physical properties such as strength and rigidity, as well as productivity, are poor.
  • the present inventors have completed this invention upon the unexpected finding that modifying the compatibility between the resin and the sizing agent that is coated during production of continuous reinforcing fibers, and the sealability during molding and of flow of the resin, can drastically reduce voids at the interface between the continuous reinforcing fibers and synthetic resin, so that press molding thereof allows production of a continuous fiber-reinforced molded resin having high strength and rigidity, while also lowering the loss tangent of the continuous fiber-reinforced molded resin so that press molding thereof allows production of a continuous fiber-reinforced molded resin having high shock absorption, and increasing the storage modulus of the continuous fiber-reinforced molded resin so that press molding thereof allows production of a continuous fiber-reinforced molded resin having high impact strength, and further that in a continuous fiber-reinforced molded resin having two or more thermoplastic resins, if the proportion of each resin at the interface regions between the continuous reinforcing fibers and resin is
  • the present invention provides the following.
  • a continuous fiber-reinforced molded resin comprising continuous reinforcing fibers with approximately circular cross-sections and a synthetic resin, wherein at the interface between each single continuous reinforcing fiber and the synthetic resin in a cross-section perpendicular to the lengthwise direction of the continuous reinforcing fiber, the number of continuous reinforcing fibers in which the void percentage within the region of the outer peripheral edge separated from the perimeter of the continuous reinforcing fiber by 1/10 of the radius of a single continuous reinforcing fiber is 10% or lower, is at least 10% of the total number of continuous reinforcing fibers.
  • a continuous fiber-reinforced molded resin comprising a thermoplastic resin and continuous reinforcing fibers, and having a loss tangent of 0.11 or lower in twisting mode.
  • a continuous fiber-reinforced molded resin comprising continuous reinforcing fibers and a thermoplastic resin, and having a storage modulus of 3.4 GPa or greater in twisting mode.
  • a continuous fiber-reinforced molded resin comprising continuous reinforcing fibers and a thermoplastic resin, and having a bending storage modulus of 22 GPa or greater.
  • a continuous fiber-reinforced molded resin comprising continuous reinforcing fibers with approximately circular cross-sections and two or more thermoplastic resins, wherein at the interface between a single continuous reinforcing fiber and the thermoplastic resin in a cross-section perpendicular to the lengthwise direction of the continuous reinforcing fiber, in a region of the outer peripheral edge separated from the perimeter of the continuous reinforcing fiber by 1/10 of the radius of a single continuous reinforcing fiber of the two or more different types, the proportion of the two or more thermoplastic resins that is occupied by resin other than the resin with the highest occupying proportion of the entire resin region, is higher than the proportion occupied by the resin with the highest occupying proportion of the entire resin region, while in the resin region other than that region of the outer peripheral edge, each of the resins other than the resin with the highest occupying proportion of the entire resin region, of the two or more thermoplastic resins, is either evenly dispersed or mixed.
  • thermoplastic resin according to any one of [20] to [22] above, wherein the melting point of the mixture of the two or more thermoplastic resins is essentially the same as the melting point of the resin with the highest occupying proportion of the entire resin region, of the two or more thermoplastic resins.
  • a method for producing a continuous fiber-reinforced resin composite material comprising the following steps:
  • thermoplastic resin having terminal functional groups that are reactive with the coupling agent, at above the melting point of the thermoplastic resin
  • thermoplastic resin a step of cooling to below the melting point of the thermoplastic resin to obtain a continuous fiber-reinforced resin composite material as a molded article.
  • thermoplastic resin is a polyamide resin
  • amount of carboxyl ends in the polyamide resin, as terminal functional groups that are reactive with the coupling agent is at least 65 ⁇ mol/g.
  • thermoplastic resin is a polyamide resin
  • amount of amino ends in the polyamide resin, as terminal functional groups that are reactive with the coupling agent is 40 ⁇ mol/g or lower.
  • a method for producing a shaped molded article of a continuous fiber-reinforced resin composite material comprising a step of heating a continuous fiber-reinforced resin composite material produced by the method according to any one of [28] to [36] at above the melting point of the thermoplastic resin, pressing it using a die, and then cooling to a temperature below the melting point of the thermoplastic resin and shaping it.
  • a method for producing a fiber-reinforced molded resin comprising a step of hot pressing reinforcing fibers and a thermoplastic resin that has a ⁇ -drop formation coefficient with the reinforcing fibers of 10 or greater, to above the melting point of the thermoplastic resin, and a step of cooling to below the crystallization temperature of the thermoplastic resin.
  • a fiber-reinforced molded resin comprising glass fibers and a polyamide resin, wherein when the fiber-reinforced molded resin is cut and the polished surface that has been polished with a force of 400 g/cm 2 is observed by SEM, at the interface between a single glass fiber and the polyamide resin in a cross-section perpendicular to the lengthwise direction of the glass fiber, the number of glass fibers in which the void percentage within the region of the outer peripheral edge separated from the perimeter of the glass fiber by 1/10 of the radius of a single glass fiber is 10% or lower, is at least 90% of the total number of glass fibers.
  • a communication device housing constituted by a composite material molded article comprising a thermoplastic resin and continuous glass reinforcing fibers, wherein the tensile strength satisfies the relationship specified by the following formula (3):
  • the electric field shielding property measured by the KEC method is 10 dB or lower in the frequency band of 1 GHz.
  • a continuous fiber-reinforced molded resin constituted by continuous reinforcing fibers and a thermoplastic resin, wherein the breaking strength due to interlayer separation is 40 MPa or higher in acoustic emission measurement.
  • the continuous fiber-reinforced molded resin of the invention has high adhesive force and affinity at the interface between the continuous reinforcing fibers and the synthetic resin, has small voids in the interface and exhibits adequate strength, rigidity and impact strength and high long-term properties, while also having a sufficiently small loss tangent and exhibiting sufficient shock absorption, having a sufficiently large storage modulus and exhibiting sufficient impact strength, and having a high resin impregnating property and high strength and rigidity.
  • FIG. 1 is a diagram illustrating the “voids” and “void percentage” in the region of the outer peripheral edge separated from the perimeter of the continuous reinforcing fiber by 1/10 of the radius of the single continuous reinforcing fiber, at the interface between a single continuous reinforcing fiber and the synthetic resin (interface region), in a cross-section perpendicular to the lengthwise direction of the continuous reinforcing fiber.
  • FIG. 2 is a photograph of the interface regions for Example 1-1, Example 2-1, Example 3-1 and Example 4-1.
  • FIG. 3 is a photograph of the interface regions for Example 1-3.
  • FIG. 4 is a photograph of the interface regions for Comparative Example 1-2.
  • FIG. 5 is a photograph of the interface regions for Comparative Example 1-3.
  • FIG. 6 is a photograph in lieu of a drawing, for illustration of the “impregnation rate” of a synthetic resin in a continuous fiber-reinforced molded resin.
  • FIG. 7 is a photograph in lieu of a drawing, showing a state where, at the interface between a single continuous reinforcing fiber and a synthetic resin in a cross-section along the lengthwise direction of a continuous reinforcing fiber with an approximately circular cross-section, in a region of the outer peripheral edge separated from the perimeter of the continuous reinforcing fiber by 1/10 of the radius of the single continuous reinforcing fiber, the proportion of the two or more thermoplastic resins that is occupied by resin other than the resin with the highest occupying proportion of the entire resin region, is higher than the proportion occupied by the resin with the highest occupying proportion of the entire resin region, but in the resin region other than that region of the outer peripheral edge, the resin other than the resin with the highest occupying proportion of the entire resin region, of the two or more thermoplastic resins, is evenly dispersed.
  • FIG. 8 is a photograph of the interface regions for Example 6-1.
  • FIG. 9 is a photograph of the interface regions for Comparative Example 6-2.
  • FIG. 10 is a photograph of the interface regions for Example 10.
  • FIG. 11 is a photograph of the interface regions for Comparative Example 10.
  • FIG. 12 is a diagram showing the shape of a smartphone housing for Example 9.
  • the continuous fiber-reinforced molded resin of the embodiment is a continuous fiber-reinforced molded resin constituted by continuous reinforcing fibers with an approximately circular cross-section and a synthetic resin, wherein preferably, the number of continuous reinforcing fibers in which the void percentage in the region of the outer peripheral edge separated from the perimeter of the continuous reinforcing fiber by 1/10 of the radius of a single continuous reinforcing fiber, at the interface between each single continuous reinforcing fiber and the synthetic resin in a cross-section perpendicular to the lengthwise direction of the continuous reinforcing fiber, is 10% or lower, is at least 10% of the total number of continuous reinforcing fibers, the loss tangent (tan ⁇ ) is 0.11 or lower with dynamic viscoelasticity measurement in twisting mode, the storage modulus is 3.4 GPa or greater with dynamic viscoelasticity measurement in twisting mode, and the storage modulus is 22 GPa or greater in bending mode.
  • thermoplastic resins preferably at the interface between a single continuous reinforcing fiber and the thermoplastic resin in a cross-section perpendicular to the lengthwise direction of the continuous reinforcing fiber, in a region of the outer peripheral edge separated from the perimeter of the continuous reinforcing fiber by 1/10 of the radius of a single continuous reinforcing fiber (also referred to as the “interface region”), the proportion of the two or more thermoplastic resins that is occupied by a resin (also referred to as “secondary resin”) other than the resin with the highest occupying proportion of the entire resin region (also referred to as “primary resin”), is higher than the proportion occupied by the resin with the highest occupying proportion of the entire resin region, while in the resin region other than that region of the outer peripheral edge (also referred to as “other resin region”), the resin (secondary resin) other than the resin with the highest occupying proportion of the entire resin region, of the two or more thermoplastic resins, is either evenly dispersed or mixed
  • thermoplastic resin having terminal functional groups that are reactive with the coupling agent, at above the melting point of the thermoplastic resin
  • thermoplastic resin a step of cooling to below the melting point of the thermoplastic resin to obtain a continuous fiber-reinforced resin composite material as a molded article.
  • the continuous fiber-reinforced molded resin of the embodiment is a continuous fiber-reinforced molded resin comprising continuous reinforcing fibers with approximately circular cross-sections and a synthetic resin, wherein continuous reinforcing fibers are present which have a void percentage of 10% or lower in the region of the outer peripheral edge that is separated from the perimeter of each continuous reinforcing fiber by 1/10 of the radius r of a single continuous reinforcing fiber (i.e., r/10) in the radial direction (also referred to as “interface region”), when observed at the interface between a single continuous reinforcing fiber and the synthetic resin in a cross-section perpendicular to the lengthwise direction of the continuous reinforcing fiber, and their number is at least 10% of the total number of continuous reinforcing fibers.
  • cross-sections of the continuous reinforcing fibers are preferably approximately circular cross-sections, they may also be ellipsoid as shown in FIG. 1 .
  • radius means the shortest distance from the center of the fiber cross-section toward the perimeter.
  • the occupying ratio of the secondary resin of the two or more thermoplastic resins is higher than the occupying ratio of the primary resin, in the interface region. This state is illustrated in FIG. 7 .
  • the void percentage in the “region of the outer peripheral edge separated from the perimeter of the continuous reinforcing fiber by 1/10 of the radius of a single continuous reinforcing fiber, as observed at the interface between a single continuous reinforcing fiber and the synthetic resin in a cross-section perpendicular to the lengthwise direction of the continuous reinforcing fiber” can be determined by the following formula:
  • Void percentage (%) (area of voids in region of outer peripheral edge separated from perimeter of continuous reinforcing fiber by 1/10 of radius of continuous reinforcing fiber)/(area of region of outer peripheral edge separated from perimeter of continuous reinforcing fiber by 1/10 of radius of continuous reinforcing fiber) ⁇ 100,
  • the void percentage is determined for the region of the outer peripheral edge separated from the perimeter of an arbitrary single continuous reinforcing fiber with an approximately circular cross-section by a distance of 1/10 of the radius (the “region of 1/10 of the diameter of a continuous reinforcing fiber” will hereunder also be referred to simply as “interface region”), and is observed for 100 arbitrary selected fibers.
  • the fibers preferably at least 10%, or 10 out of every 100, more preferably at least 20%, even more preferably at least 50%, yet more preferably at least 70% and most preferably at least 90%, of the fibers have a void percentage of 10% or lower in the region of 1/10 of the diameter of the continuous reinforcing fiber, from the viewpoint of increasing the rigidity and strength of the molded article.
  • the void percentage in the region of 1/10 of the diameter of the continuous reinforcing fiber is preferably 5% or lower, more preferably 2% or lower and even more preferably 1% or lower, from the viewpoint of increasing the rigidity and strength of the molded article.
  • the sizing agent coated during production of the glass fiber is selected to be one such that the ⁇ -drop formation coefficient between the sizing agent and the synthetic resin is 10 or greater, and their compatibility is satisfactory
  • the molding method selected is either a molding method allowing the die interior to be sealed during molding, such as using an inlay die, or a molding method using a double belt press with adjustable pressure, whereby leakage of the resin is prevented and variation in the volume of the continuous fiber-reinforced molded resin occupied by the glass fibers (Vf, also known as the volume content) before and after molding is reduced, and molding is carried out under temperature conditions suited for the sizing agent.
  • the loss tangent in twisting mode can be calculated from the peak top value of the loss tangent based on viscoelasticity measurement of the continuous fiber-reinforced molded resin cut with a band saw at 0° and 90° directions with respect to the continuous fiber in twisting mode, under a nitrogen atmosphere and with a constant temperature-elevating rate, for example.
  • the loss tangent of the continuous fiber-reinforced molded resin of the embodiment in twisting mode is preferably 0.11 or lower, more preferably 0.10 or lower, even more preferably 0.095 or lower, even more preferably 0.090 or lower and most preferably 0.087 or lower.
  • the temperature at which the peak top of the loss tangent of the continuous fiber-reinforced molded resin of the embodiment in twisting mode is exhibited is preferably 78° C. or higher, more preferably 80° C. or higher, even more preferably 82° C. or higher and most preferably 84° C. or higher.
  • the difference between the two peak tops is preferably no greater than 80° C., more preferably no greater than 60° C., even more preferably no greater than 50° C. and most preferably no greater than 35° C.
  • the sizing agent coated during production of the glass fiber is selected to be one such that the ⁇ -drop formation coefficient between the sizing agent and the synthetic resin is 10 or greater, and their compatibility is satisfactory, while the molding method selected is either a molding method allowing the die interior to be sealed during molding, such as using an inlay die, or a molding method using a double belt press with adjustable pressure, whereby leakage of the resin is prevented and variation in the volume of the continuous fiber-reinforced molded resin occupied by the glass fibers (Vf, also known as the volume content) before and after molding is reduced, and molding is carried out under temperature conditions suited for the sizing agent.
  • Vf also known as the volume content
  • the storage modulus in twisting mode can be calculated from the peak top value of the storage modulus when the storage modulus is plotted against each temperature, based on viscoelasticity measurement of the continuous fiber-reinforced molded resin cut with a band saw at 0° and 90° directions with respect to the continuous fiber in twisting mode, under a nitrogen atmosphere and with a constant temperature-elevating rate, for example.
  • the storage modulus of the continuous fiber-reinforced molded resin of the embodiment in twisting mode is preferably 3.4 GPa or greater, more preferably 3.5 GPa or greater, even more preferably 4.0 GPa or greater, yet more preferably 4.5 GPa or greater, even yet more preferably 6.0 GPa or greater and most preferably 7.0 GPa or greater.
  • the storage modulus when measurement of the storage modulus is carried out using a test piece cut in the 45° direction (diagonal direction) of the continuous fiber of the continuous fiber-reinforced molded resin is preferably at least 1.5 times, more preferably at least 1.6 times, even more preferably at least 1.7 times and most preferably at least 1.9 times the storage modulus when the measurement is carried out using test pieces cut in the 0° and 90° directions.
  • the storage modulus at 150° C. is preferably at least 25% and more preferably at least 26% of the maximum storage modulus.
  • the shear viscosity is preferably 330 MPa ⁇ s ⁇ 1 or greater, more preferably 470 MPa ⁇ s ⁇ 1 or greater, even more preferably 500 MPa ⁇ s ⁇ 1 or greater and most preferably 700 MPa ⁇ s ⁇ 1 or greater.
  • the sizing agent coated during production of the glass fiber is selected to be one such that the ⁇ -drop formation coefficient between the sizing agent and the synthetic resin is 10 or greater, and their compatibility is satisfactory
  • the molding method selected is either a molding method allowing the die interior to be sealed during molding, such as using an inlay die, or a molding method using a double belt press with adjustable pressure, whereby leakage of the resin is prevented and variation in the volume of the continuous fiber-reinforced molded resin occupied by the glass fibers (Vf, also known as the volume content) before and after molding is reduced, and molding is carried out under temperature conditions suited for the sizing agent.
  • the bending storage modulus can be calculated from the maximum storage modulus when the storage modulus is plotted against each temperature, based on viscoelasticity measurement of the continuous fiber-reinforced molded resin cut with a band saw at 0° and 90° directions with respect to the continuous fiber in bending mode, under a nitrogen atmosphere and with a constant temperature-elevating rate, for example.
  • the bending storage modulus of the continuous fiber-reinforced molded resin of the embodiment is preferably 22 GPa or greater, more preferably 23 GPa or greater, even more preferably 25 GPa or greater, yet more preferably 31 GPa or greater and most preferably 36 GPa or greater.
  • the bending storage modulus when measured at 150° C. is preferably at least 76% of the bending storage modulus at 30° C.
  • the bending storage modulus when measurement of the bending storage modulus is carried out using a test piece cut in the 45° direction (diagonal direction) of the continuous fiber of the continuous fiber-reinforced molded resin, is preferably at least 58%, more preferably at least 60% and even more preferably at least 62% of the bending storage modulus when the measurement is carried out using test pieces cut in the 0° or 90° direction.
  • the tensile storage modulus and tensile loss tangent can be calculated based on viscoelasticity measurement of the continuous fiber-reinforced molded resin cut with a band saw at 0° and 90° directions with respect to the continuous fiber in tension mode, under a nitrogen atmosphere and with a constant temperature-elevating rate, for example.
  • the tensile storage modulus of the continuous fiber-reinforced molded resin of the embodiment at 50° C. is preferably 22 GPa or greater, more preferably 25 GPa or greater, even more preferably 30 GPa or greater, yet more preferably 32 GPa or greater, even yet more preferably 35 GPa or greater and most preferably 40 GPa or greater.
  • the maximum tensile loss tangent can be determined as the maximum point on the plot of the loss tangent at each temperature, obtained by the aforementioned measurement.
  • the maximum loss tangent of the continuous fiber-reinforced molded resin of the embodiment is preferably 0.037 or lower, more preferably 0.035 or lower and even more preferably 0.032 or lower.
  • the temperature at which the values of the tensile storage modulus and bending storage modulus are reversed is preferably 95° C. or higher, more preferably 100° C. or higher and even more preferably 105° C. or higher, when the tensile storage modulus and bending storage modulus are plotted against each temperature.
  • the sizing agent coated during production of the glass fibers is selected to be one such that the ⁇ -drop formation coefficient between the sizing agent and the synthetic resin is 10 or greater, and their compatibility is satisfactory
  • the molding method selected is either a molding method allowing the die interior to be sealed during molding to inhibit flow of the resin, such as using an inlay die, or a molding method using a double belt press with adjustable pressure, whereby leakage of the resin is prevented and variation in the volume of the continuous fiber-reinforced molded resin occupied by the glass fibers (Vf, also known as the volume content) before and after molding is reduced, and molding is carried out while forming a satisfactory boundary interface, under temperature conditions suited for the sizing agent.
  • the proportion of the region of the outer peripheral edge of the continuous fiber-reinforced molded resin of the embodiment that is occupied by each thermoplastic resin can be determined by cutting a cross-section in the thickness direction of the continuous fiber-reinforced molded resin (a cross-section perpendicular to the lengthwise direction of the continuous reinforcing fibers), embedding it in an epoxy resin and polishing it while taking care that the continuous reinforcing fibers are not damaged, and then taking a mapping image of the cross-section with a laser Raman microscope and identifying the type of resins in the fiber-reinforced resin from the obtained image and spectrum, and calculating the area of each by image processing with imageJ software.
  • the distribution of the thermoplastic resins in the resin region other than the interface region of the fiber-reinforced molded resin can be determined, for example, by polishing a cross-section (cross-section perpendicular to the lengthwise direction of the continuous reinforcing fibers) of the continuous fiber-reinforced molded resin that has been cut at a cross-section in the thickness direction (a cross-section perpendicular to the lengthwise direction of the continuous reinforcing fibers), with a force of 125 g/cm 2 on the polished surface, for 10 minutes with #220 waterproof paper, 10 minutes with #1200 waterproof paper, 5 minutes with #2000 waterproof paper, 10 minutes with a silicon carbide film having a particle size of 9 ⁇ m, 10 minutes with an alumina film having a particle size of 5 ⁇ m, 5 minutes with an alumina film having a particle size of 3 ⁇ m, 5 minutes with an alumina film having a particle size of 1 ⁇ m, and 5 minutes with colloidal silica having a particle size of 0.1
  • the continuous fiber-reinforced molded resin of the embodiment is preferably one wherein the volume content Vf of the continuous reinforcing fibers in the continuous fiber-reinforced molded resin is 40% or higher, more preferably 45% or higher, even more preferably 50% or higher, yet more preferably 55% or higher and most preferably 65% or higher.
  • the tensile stress of the continuous fiber-reinforced molded resin is preferably 480 MPa or higher, more preferably 525 MPa or higher, even more preferably 600 MPa or higher and most preferably 620 MPa or higher, as the average value from testing in different directions in which the glass fibers are essentially oriented.
  • the flexural modulus of the continuous fiber-reinforced molded resin is preferably 22 GPa or greater, more preferably 27 GPa or greater, even more preferably 30 GPa or greater and most preferably 35 GPa or greater, as the average value from testing in different directions in which the glass fibers are essentially oriented.
  • the tensile stress and flexural modulus are the values when the continuous reinforcing fibers in the continuous fiber-reinforced molded resin are oriented in essentially biplanar directions, being average values for testing in biplanar directions parallel to the continuous reinforcing fibers.
  • 2/3 stress or rigidity is preferred, and for an n-directional material, 2/n stress or rigidity is preferred.
  • the value of the number of directions in which the glass fibers are essentially oriented multiplied by the average value of the tensile stress when testing in different directions in which the glass fibers of the continuous fiber-reinforced molded resin are essentially oriented is preferably 960 MPa or higher, more preferably 1050 MPa or higher, even more preferably 1200 MPa or higher and most preferably 1240 MPa or higher.
  • the value of the number of directions in which the glass fibers are essentially oriented multiplied by the average value of the flexural stress when testing in different directions in which the glass fibers of the continuous fiber-reinforced molded resin are essentially oriented is preferably 1260 MPa or higher, more preferably 1400 MPa or higher, even more preferably 1600 MPa or higher and most preferably 1700 MPa or higher.
  • the value of the flexural modulus of the continuous fiber-reinforced molded resin multiplied by the number of directions in which the glass fibers are essentially oriented is preferably 44 GPa or greater, more preferably 54 GPa or greater, even more preferably 60 GPa or greater and most preferably 70 GPa or greater.
  • the elasticity index of the continuous fiber-reinforced molded resin defined by the following formula:
  • Elasticity index (average value of elastic modulus in directions parallel to the directions in which glass fibers are essentially oriented ⁇ number of directions in which glass fibers are essentially oriented)/(Vf ⁇ elastic modulus of glass fibers)
  • the continuous fiber-reinforced molded resin of the embodiment has an interlayer separation-induced breaking strength of preferably 40 MPa or higher and more preferably 50 MPa or higher.
  • Measurement by the acoustic emission method can be carried out by attaching an AE sensor in an interlaminar shear test (JIS K7078).
  • the form of the continuous fiber-reinforced molded resin is not particularly restricted, and the following forms are possible.
  • it may be in the form of a woven fabric or knitted fabric, a braid or a pipe form of the reinforcing fibers in combination with a resin, in the form of reinforcing fibers aligned in one direction and composited with a resin, in the form of yarns comprising reinforcing fibers and a resin aligned and molded in one direction, or in the form of yarn comprising reinforcing fibers and a resin that has been molded as a woven fabric or knitted fabric, a braid or a pipe form.
  • the form of the intermediate material of the continuous fiber-reinforced molded resin before molding may be combined filament yarn comprising continuous reinforcing fibers and resin fibers, coating yarn wherein the periphery of a continuous reinforcing fiber bundle is covered with a resin, a tape-like form with the resin impregnating the continuous reinforcing fibers beforehand, continuous reinforcing fibers sandwiched between resin films, resin powder adhering to continuous reinforcing fibers, a continuous reinforcing fiber bundle as the core material surrounded with a resin fiber braid, or a reinforcing fiber bundle impregnated with a resin beforehand.
  • thermoplastic resin having terminal functional groups that are reactive with the coupling agent, at above the melting point of the thermoplastic resin
  • thermoplastic resin a step of cooling to below the melting point of the thermoplastic resin to obtain a continuous fiber-reinforced resin composite material as a molded article.
  • the amount of terminal functional groups of the continuous fiber-reinforced resin composite material after hot pressing is preferably less than the amount of terminal functional groups in the thermoplastic resin before hot pressing from the viewpoint of adhesion between the thermoplastic resin and the continuous reinforcing fibers, the amount of terminal functional groups of the continuous fiber-reinforced resin composite material after hot pressing being preferably 90% or lower and more preferably 85% or lower compared to the amount of terminal functional groups in the thermoplastic resin before hot pressing.
  • the flow rate of the thermoplastic resin during hot pressing is preferably 10% or lower, more preferably 8% or lower, even more preferably 5% or lower and most preferably 3% or lower.
  • the reactive terminal functional groups are maleic acid grafted onto the polypropylene resin as the main component.
  • the flow rate of the thermoplastic resin during hot pressing can be determined as (weight of thermoplastic resin burrs produced during hot pressing)/(weight of thermoplastic resin before hot pressing).
  • the method of hot pressing is not particularly restricted, but a hot pressing method using a double belt press is preferred from the viewpoint of productivity.
  • the reinforcing fibers and thermoplastic resin may be fed out from multiple rolls and introduced into a double belt press apparatus, or the reinforcing fibers and thermoplastic resin cut to a desired size may be stacked in the desired number and introduced.
  • a guide sheet such as a TEFLON R sheet may also be introduced in front of and behind the base material.
  • Another preferred hot pressing method is one carried out with a die. Pressing with a die is not particularly restricted, and any of the following methods are possible.
  • the base material that is to compose the continuous fiber-reinforced molded resin may be cut to match the desired molded article shape and layered in the necessary number for the thickness of the target product, and set in a manner conforming to the die shape.
  • Cutting of the base material may be carried out one at a time, or any number may be stacked and cut together. From the viewpoint of productivity, a plurality are preferably cut in a stacked state. Any method may be used for cutting, examples of which include methods using a water jet, blade press machine, hot blade press machine, laser or plotter. A hot blade press machine is preferred, for an excellent cross-sectional shape, and also better handleability by welding of the edges when a multiple stack is cut. A suitable cutting shape can be adjusted by repeated trial and error, but it is preferably set by carrying out a simulation with CAE (computer aided engineering), matching the die shape.
  • CAE computer aided engineering
  • the die After the base material has been set in the die, the die is closed and the material is pressed (compressed). The die is adjusted to a temperature at or above the melting point of the thermoplastic resin composing the continuous fiber-reinforced molded resin, to melt the thermoplastic resin and shape it.
  • the mold clamping pressure is not particularly stipulated but is preferably 1 MPa or higher and more preferably 3 MPa or higher.
  • the mold is clamped once for compression molding to remove the gas, after which the die mold clamping pressure is released. From the viewpoint of exhibiting strength, the compression molding time is preferably as long as possible in a range that does not result in heat degradation of the thermoplastic resin, and from the viewpoint of productivity, it is preferably no longer than 2 minutes and more preferably no longer than 1 minute.
  • the base material is set into a die and the die is closed and pressurized, and after a predetermined time has elapsed, it may be filled with a predetermined thermoplastic resin composition that is injected in and molded, joining the thermoplastic resin with the predetermined thermoplastic resin composition to produce a hybrid molded article.
  • the timing for injection filling of the predetermined thermoplastic resin composition will largely depend on the interfacial strength between both thermoplastic resins.
  • the timing for injection filling of the predetermined thermoplastic resin composition is preferably no longer than 30 seconds after the die temperature has increased above the melting point and glass transition temperature of the thermoplastic resin, after the base material has been set in the die and the die has been closed.
  • the die temperature during injection filling of the predetermined thermoplastic resin composition is preferably at or above the melting point or glass transition temperature of the thermoplastic resin composing the continuous fiber-reinforced molded resin. More preferably, it is at or above the melting point +10° C. or the glass transition temperature +10° C., even more preferably at or above the melting point +20° C. or the glass transition temperature +20° C., and yet more preferably at or above the melting point +30° C. or the glass transition temperature +30° C., of the thermoplastic resin composing the continuous fiber-reinforced molded resin.
  • the joining section between the thermoplastic resin composing the continuous fiber-reinforced molded resin and the thermoplastic resin composition formed by injection molding preferably has an irregular structure where both are combined.
  • the die temperature is at or above the melting point of the injected thermoplastic resin composition, and for the resin to be held at high pressure during injection molding, such as 1 MPa or higher.
  • the holding pressure is preferably 5 MPa or higher and more preferably 10 MPa or higher.
  • Holding for a long holding pressure time such as 5 seconds or longer, preferably 10 seconds or longer and more preferably a period until the die temperature falls below the melting point of the thermoplastic resin composition, is preferred from the viewpoint of increasing the interfacial strength.
  • thermoplastic resin composition for injection molding to be used for production of a hybrid molded article is not particularly restricted so long as it is a thermoplastic resin composition that can be used in ordinary injection molding.
  • thermoplastic resin compositions include, but are not limited to, resin compositions of one or mixtures of two or more from among polyethylene, polypropylene, polyvinyl chloride, acrylic resin, styrene-based resin, polyethylene terephthalate, polybutylene terephthalate, polyallylate, polyphenylene ether, modified polyphenylene ether resin, total aromatic polyester, polyacetal, polycarbonate, polyetherimide, polyethersulfone, polyamide-based resin, polysulfone, polyether ether ketone and polyether ketone.
  • thermoplastic resin compositions may also contain various fillers.
  • Such fillers include staple fiber and long fiber materials that are discontinuous reinforcing materials of the same types of materials as the reinforcing fibers.
  • the same sizing agent may be used as is coated onto the continuous reinforcing fibers composing the continuous fiber-reinforced molded resin of the embodiment.
  • the sizing agent preferably comprises a (silane) coupling agent, a lubricating agent and a binding agent.
  • the type of (silane) coupling agent, lubricating agent and binding agent used may be the same as in the sizing agent for the continuous reinforcing fibers described above.
  • thermoplastic resin composition to be used in injection molding is preferably similar to, and more preferably identical to, the thermoplastic resin forming the continuous fiber-reinforced molded resin, from the viewpoint of interfacial strength between the continuous fiber-reinforced molded resin part and the injection-molded thermoplastic resin composition part.
  • polyamide 66 fibers are used as the thermoplastic resin forming the continuous fiber-reinforced molded resin, it is preferred to use polyamide 66 for the resin material of the thermoplastic resin composition for injection molding.
  • Other methods include a method of molding by setting the base material in a die and compressing it with a double belt press machine, or a method of setting a frame surrounding the four sides of a set base material and compression molding it with a double belt press machine, or a method of molding by preparing a heating compression molding machine set to one or more temperatures and a cooling compression molding machine set to one or more temperatures, and loading the die in which the base material has been set into each compression molding machine in order for molding.
  • the impregnation rate of the thermoplastic resin in the continuous fiber-reinforced molded resin is determined by the proportion of voids in a cross-section of the continuous fiber-reinforced molded resin. Specifically, it is calculated by cutting the continuous fiber-reinforced molded resin at an arbitrary location, embedding it in an epoxy resin and polishing it, and then using analysis software to analyze an image obtained by optical microscope observation.
  • the impregnation rate (%) is calculated by the following formula:
  • Impregnation rate (%) ⁇ 1 ⁇ (void area/continuous reinforcing fiber bundle area) ⁇ 100
  • the impregnation rate of the continuous fiber-reinforced molded resin of the embodiment is preferably 98% or higher, more preferably 99% or higher, even more preferably 99.5% or higher and most preferably 99.9% or higher.
  • the continuous reinforcing fibers used may generally be any ones used for continuous fiber-reinforced molded resins.
  • Continuous reinforcing fibers include, but are not limited to, glass fibers, carbon fibers, plant fibers, aramid fibers, ultra-high strength polyethylene fibers, polybenzazole fibers, liquid crystal polyester fibers, polyketone fibers, metal fibers and ceramic fibers.
  • Glass fibers, carbon fibers, plant fibers and aramid fibers are preferred from the viewpoint of mechanical properties, thermal properties and general utility, while glass fibers are preferred from the viewpoint of productivity.
  • a sizing agent may be used, the sizing agent preferably comprising a silane coupling agent, a lubricating agent and a binding agent. If the sizing agent is one that binds strongly to the resin coating the continuous reinforcing fibers, it will be possible to obtain a continuous fiber-reinforced molded resin with a low void percentage, and when a thermoplastic resin is used as the synthetic resin, the sizing agent is preferably a sizing agent for thermoplastic resins.
  • a sizing agent for thermoplastic resins is one such that when the continuous reinforcing fibers are raised in temperature to 300° C.
  • the rigidity of the continuous reinforcing fibers is greater than the rigidity of the continuous reinforcing fibers before heating.
  • the sizing agent for thermoplastic resins must be selected as one in which the silane coupling agent easily bonds with the terminal carboxyl groups and amino groups of the polyamide resin. Specific examples include ⁇ -aminopropyltrimethoxysilane and epoxysilane.
  • the binding agent used is a resin having good wettability with or similar surface tension as the polyamide resin.
  • a polyurethane resin emulsion or polyamide resin emulsion, or a modified form of the same, may be selected.
  • a lubricating agent that does not inhibit the silane coupling agent and binding agent an example of which is carnauba wax.
  • the sizing agent preferably diffuses at least 50%, more preferably at least 70%, even more preferably at least 80% and most preferably at least 90%, in the thermoplastic resin during hot pressing. Diffusion of the sizing agent can be determined for the molded article by dissolving the matrix resin with a good solvent and performing XPS measurement of the remaining reinforcing fibers, and when the matrix resin is a polyamide, it is preferred to use HFIP or phenol.
  • the sizing agent diffuses at least 90% in the thermoplastic resin during hot pressing, and terminal groups that are reactive with the coupling agent among the terminal functional groups of the thermoplastic resin are decreased before and after hot pressing, then the coupling agent has bonded with the terminal functional groups of the thermoplastic resin.
  • the continuous reinforcing fibers may also be coated with a catalyst that promotes reaction between the coupling agent and the terminal functional groups of the thermoplastic resin, and when glass fibers are selected as the continuous reinforcing fibers and a polyamide resin is selected as the thermoplastic resin, for example, examples of such a catalyst include phosphoric compounds such as sodium hypophosphite, which promote bonding reaction between the amino groups of the silane coupling agent and the terminal carboxyl groups of the polyamide resin.
  • a silane coupling agent is usually used as a surface treatment agent for glass fibers, where it contributes to increased interfacial bonding strength.
  • silane coupling agents include, but are not limited to, aminosilanes such as ⁇ -aminopropyltrimethoxysilane and N- ⁇ -(aminoethyl)- ⁇ -aminopropylmethyldimethoxysilane; mercaptosilanes such as ⁇ -mercaptopropyltrimethoxysilane and ⁇ -mercaptopropyltriethoxysilane; epoxysilanes; and vinylsilanes and maleic acid.
  • aminosilanes such as ⁇ -aminopropyltrimethoxysilane and N- ⁇ -(aminoethyl)- ⁇ -aminopropylmethyldimethoxysilane
  • mercaptosilanes such as ⁇ -mercaptopropyltrimethoxysilane and ⁇ -mercaptopropyltriethoxysilane
  • epoxysilanes epoxys and maleic acid.
  • a lubricating agent contributes to improved openability of the glass fibers.
  • the lubricating agent used may be a common liquid or solid lubricating material, selected depending on the purpose, and it may be, but is not limited to, animal- or plant-based or mineral-based waxes such as carnauba wax or lanolin wax; and surfactants such as fatty acid amides, fatty acid esters, fatty acid ethers, aromatic esters and aromatic ethers.
  • a binding agent contributes to improved bundling and increased interfacial bonding strength of glass fibers.
  • a binding agent that is used may be a polymer or thermoplastic resin, depending on the purpose.
  • Polymers to be used as binding agents include, but are not limited to, acrylic acid homopolymers, copolymers of acrylic acid and other copolymerizable monomers, and salts of these with primary, secondary or tertiary amines.
  • Suitable examples to be used include polyurethane-based resins synthesized from isocyanates such as m-xylylene diisocyanate, 4,4′-methylenebis(cyclohexylisocyanate) and isophorone diisocyanate, and polyester-based or polyether-based diols.
  • An acrylic acid homopolymer has a weight-average molecular weight of preferably 1,000 to 90,000 and more preferably 1,000 to 25,000.
  • copolymerizable monomers for formation of copolymers of acrylic acid with other copolymerizable monomers include, but are not limited to, one or more monomers with hydroxyl and/or carboxyl groups, selected from the group consisting of acrylic acid, maleic acid, methacrylic acid, vinylacetic acid, crotonic acid, isocrotonic acid, fumaric acid, itaconic acid, citraconic acid and mesaconic acid (where acrylic acid alone is excluded).
  • Preferred copolymerizable monomers are one or more ester-based monomers.
  • Primary, secondary or tertiary amine salts of acrylic acid homopolymers and copolymers include, but are not limited to, triethylamine salts, triethanolamine salt and glycine salts.
  • the neutralization degree is preferably 20 to 90% and more preferably 40 to 60%, from the viewpoint of improving stability of the mixed solution with other agents (such as silane coupling agents), and reducing amine odor.
  • the weight-average molecular weight of a polymer of acrylic acid forming a salt is not particularly restricted but is preferably in the range of 3,000 to 50,000. It is preferably 3,000 or greater from the viewpoint of improved bundling of glass fibers, and preferably 50,000 or lower from the viewpoint of improving the properties as a composite molded article.
  • thermoplastic resins to be used as binding agents include, but are not limited to, polyolefin-based resins, polyamide-based resins, polyacetal-based resins, polycarbonate-based resins, polyester-based resins, polyether ketones, polyether ether ketones, polyether sulfones, polyphenylene sulfide, thermoplastic polyetherimides, thermoplastic fluorine-based resins, and modified thermoplastic resins obtained by modifying such resins.
  • thermoplastic resin used as a binding agent is preferably a thermoplastic resin and/or modified thermoplastic resin of the same type as the resin covering the periphery of the continuous reinforcing fibers, since this will improve adhesion between the glass fibers and thermoplastic resin after a composite molded article has been formed.
  • thermoplastic resin of the binding agent it is preferred to use a modified thermoplastic resin as the thermoplastic resin of the binding agent, from the viewpoint of reducing the ratio of emulsifier component or limiting the need for an emulsifier.
  • a modified thermoplastic resin is one that has been copolymerized with a different monomer component other than a monomer component that can form the main chain of the thermoplastic resin, having its hydrophilicity, crystallinity or thermodynamic properties modified, in order to alter the properties of the thermoplastic resin.
  • modified thermoplastic resins to be used as binding agents include, but are not limited to, modified polyolefin-based resins, modified polyamide-based resins and modified polyester-based resins.
  • a modified polyolefin-based resin for the binding agent is a copolymer of an olefin-based monomer such as ethylene or propylene and a monomer that is copolymerizable with the olefin-based monomer, such as an unsaturated carboxylic acid, and it can be produced by a known method. It may be a random copolymer obtained by copolymerization of an olefin-based monomer and an unsaturated carboxylic acid, or a graft copolymer obtained by grafting an unsaturated carboxylic acid onto an olefin.
  • olefin-based monomers examples include, but are not limited to, ethylene, propylene and 1-butene. These may be used alone, or two or more may be used in combination.
  • monomers that are copolymerizable with olefin-based monomers include unsaturated carboxylic acids such as acrylic acid, maleic acid, maleic anhydride, methacrylic acid, vinylacetic acid, crotonic acid, isocrotonic acid, fumaric acid, itaconic acid, citraconic acid and mesaconic acid, any of which may be used alone or in combinations of two or more.
  • the copolymerization ratio of the olefin-based monomer and the monomer that is copolymerizable with the olefin-based monomer is preferably 60 to 95 mass % of the olefin-based monomer and 5 to 40 mass % of the monomer that is copolymerizable with the olefin-based monomer, and more preferably 70 to 85 mass % of the olefin-based monomer and 15 to 30 mass % of the monomer that is copolymerizable with the olefin-based monomer, with the total mass of the copolymerization as 100 mass %.
  • the olefin-based monomer is 60 mass % or greater, affinity with the matrix will be satisfactory, and if the mass percentage of the olefin-based monomer is 95 mass % or lower, the water dispersibility of the modified polyolefin-based resin will be satisfactory and it will be easier to achieve uniform application on the continuous reinforcing fibers.
  • the modified polyolefin-based resin to be used as the binding agent may have the modified groups such as carboxyl groups, which have been introduced by copolymerization, neutralized with a basic compound.
  • basic compounds include, but are not limited to, alkali compounds such as sodium hydroxide and potassium hydroxide; ammonia; and amines such as monoethanolamine and diethanolamine.
  • the weight-average molecular weight of the modified polyolefin-based resin to be used as a binding agent is not particularly restricted, but it is preferably 5,000 to 200,000 and more preferably 50,000 to 150,000. It is preferably 5,000 or greater from the viewpoint of improved bundling of glass fibers, and preferably 200,000 or lower from the viewpoint of emulsified stability in water-dispersible form.
  • a modified polyamide-based resin to be used as a binding agent is a modified polyamide compound having a hydrophilic group such as a polyalkylene oxide chain or tertiary amine component introduced into the molecular chain, and it can be produced by a publicly known method.
  • a polyalkylene oxide chain When a polyalkylene oxide chain is to be introduced into the molecular chain, it is produced, for example, by copolymerization of a compound in which all or a portion of polyethylene glycol or polypropylene glycol has been modified to a diamine or dicarboxylic acid.
  • a tertiary amine component For introduction of a tertiary amine component, it is produced by copolymerization of aminoethylpiperazine, bisaminopropylpiperazine or ⁇ -dimethylamino ⁇ -caprolactam, for example.
  • a modified polyester-based resin to be used as a binding agent is a resin that is a copolymer of a polycarboxylic acid or its anhydride and a polyol, and that has a hydrophilic group in the molecular skeleton including the ends, and it can be produced by a publicly known method.
  • hydrophilic groups include polyalkylene oxides, sulfonic acid salts, carboxyl groups, and their neutral salts.
  • Polycarboxylic acids and their anhydrides include aromatic dicarboxylic acids, sulfonic acid salt-containing aromatic dicarboxylic acids, aliphatic dicarboxylic acids, alicyclic dicarboxylic acids and trifunctional or greater polycarboxylic acids.
  • aromatic dicarboxylic acids include, but are not limited to, phthalic acid, terephthalic acid, isophthalic acid, orthophthalic acid, 1,5-naphthalenedicarboxylic acid, 2,6-naphthalenedicarboxylic acid and phthalic anhydride.
  • sulfonic acid salt-containing aromatic dicarboxylic acids include, but are not limited to, sulfoterephthalic acid salts, 5-sulfoisophthalic acid salts and 5-sulfoorthophthalic acid salts.
  • aliphatic dicarboxylic acids or alicyclic dicarboxylic acids include, but are not limited to, fumaric acid, maleic acid, itaconic acid, succinic acid, adipic acid, azelaic acid, sebacic acid, dimer acid, 1,4-cyclohexanedicarboxylic acid, succinic anhydride and maleic anhydride.
  • trifunctional or greater polycarboxylic acids include, but are not limited to, trimellitic acid, pyromellitic acid, trimellitic anhydride and pyromellitic anhydride.
  • the modified polyester-based resin From the viewpoint of increasing the heat resistance of the modified polyester-based resin, preferably 40 to 99 mol % of the total polycarboxylic acid component consists of aromatic dicarboxylic acids. From the viewpoint of emulsified stability when the modified polyester-based resin is in the form of an aqueous dispersion, preferably 1 to 10 mol % of the total polycarboxylic acid component is sulfonic acid salt-containing aromatic dicarboxylic acids.
  • the polyol forming the modified polyester-based resin may be a diol or a trifunctional or greater polyol.
  • diols examples include, but are not limited to, ethylene glycol, diethylene glycol, polyethylene glycol, propylene glycol, polypropylene glycol, polybutylene glycol, 1,3-propanediol, 1,4-butanediol, 1,6-hexanediol, neopentyl glycol, polytetramethylene glycol, 1,4-cyclohexanediol, 1,4-cyclohexanedimethanol, bisphenol A, and their alkylene oxide addition products.
  • Trifunctional or greater polyols include trimethylolpropane, glycerin and pentaerythritol.
  • the copolymerization ratio of the polycarboxylic acid or its anhydride and the polyol forming the modified polyester-based resin is preferably 40 to 60 mass % of the polycarboxylic acid or its anhydride and 40 to 60 mass % of the polyol and more preferably 45 to 55 mass % of the polycarboxylic acid or its anhydride and 45 to 55 mass % of the polyol, with the total mass of the copolymerizing component as 100 mass %.
  • the weight-average molecular weight of the modified polyester-based resin is preferably 3,000 to 100,000 and more preferably 10,000 to 30,000. It is preferably 3,000 or greater from the viewpoint of improved bundling of the glass fibers, and preferably 100,000 or lower from the viewpoint of emulsified stability in water-dispersible form.
  • the polymer and thermoplastic resin used as the binding agent may be used alone, or two or more may be used in combination.
  • one or more polymers selected from among acrylic acid homopolymers, copolymers of acrylic acid and other copolymerizable monomers, and salts thereof with primary, secondary and tertiary amines, at 50 mass % or greater or 60 mass % or greater, with the entire amount of the binding agent as 100 mass %.
  • the sizing agent of the glass fibers preferably contains 0.1 to 2 mass % of a silane coupling agent, 0.01 to 1 mass % of a lubricating agent and 1 to 25 mass % of a binding agent, and preferably the components are diluted with water for adjustment of the total mass to 100 mass %.
  • the content of the silane coupling agent in the sizing agent for glass fibers is preferably 0.1 to 2 mass %, more preferably 0.1 to 1 mass % and even more preferably 0.2 to 0.5 mass %, from the viewpoint of improving bundling of the glass fibers, increasing the interfacial bonding strength and increasing the mechanical strength of the composite molded article.
  • the content of the lubricating agent in the sizing agent for glass fibers is preferably 0.01 mass % or greater and more preferably 0.02 mass % or greater, and from the viewpoint of increasing the interfacial bonding strength and increasing the mechanical strength of the composite molded article it is preferably 1 mass % or lower and more preferably 0.5 mass % or lower.
  • the content of the binding agent in the sizing agent for glass fibers is preferably 1 to 25 mass %, more preferably 3 to 15 mass % and even more preferably 3 to 10 mass %, from the viewpoint of controlling bundling of the glass fibers, increasing the interfacial bonding strength and increasing the mechanical strength of the composite molded article.
  • the sizing agent for glass fibers may be prepared into any form such as an aqueous solution, a colloidal dispersion or an emulsion using an emulsifier, depending on the usage, but it is preferably in the form of an aqueous solution from the viewpoint of increasing the dispersion stability of the sizing agent and increasing the heat resistance.
  • Glass fibers used as continuous reinforcing fibers in the continuous fiber-reinforced molded resin of the embodiment can be continuously obtained by drying glass fibers produced using a known method employing a roller-type applicator in a production process for known glass fibers, and applying the sizing agent to the glass fibers.
  • the sizing agent is applied at preferably 0.1 to 3 mass %, more preferably 0.2 to 2 mass % and even more preferably 0.2 to 1 mass %, as the total mass of the silane coupling agent, lubricating agent and binding agent, with respect to 100 mass % of the glass fibers.
  • the sizing agent coverage is preferably 0.1 mass % or greater, as the total mass of the silane coupling agent, lubricating agent and binding agent with respect to 100 mass % of the glass fibers, and it is also preferably 3 mass % or lower from the viewpoint of yarn handleability.
  • the sizing agent preferably comprises a coupling agent, a lubricating agent and a binding agent.
  • the types of sizing agent, lubricating agent and binding agent are not particularly restricted, and publicly known agents may be used. Specific materials that may be used include the materials mentioned in Japanese Unexamined Patent Publication No. 2015-101794.
  • the coupling agent may be selected as one with good compatibility with the hydroxyl groups present on the surfaces of the carbon fibers
  • the binding agent may be selected as one having good wettability with and similar surface tension to the selected synthetic resin
  • the lubricating agent may be selected as one that does not inhibit the coupling agent and binding agent.
  • the type and coverage of the sizing agent used on the glass fibers and carbon fibers may be selected as appropriate depending on the properties of the continuous reinforcing fibers, but the type and coverage of the sizing agent are preferably for a sizing agent used for carbon fibers.
  • the continuous reinforcing fibers are preferably multifilaments composed of a plurality of reinforcing fibers, with the filament number preferably being 30 to 15,000, from the viewpoint of handleability.
  • the monofilament diameter of the continuous reinforcing fibers is preferably 2 to 30 ⁇ m, more preferably 4 to 25 ⁇ m, even more preferably 6 to 20 ⁇ m and most preferably 8 to 18 ⁇ m, from the viewpoint of strength and manageability.
  • the product RD of the monofilament diameter R ( ⁇ m) and the density D (g/cm 3 ) of the continuous reinforcing fibers is preferably 5 to 100 ⁇ m ⁇ g/cm 3 , more preferably 10 to 50 ⁇ m ⁇ g/cm 3 , even more preferably 15 to 45 ⁇ m ⁇ g/cm 3 and yet more preferably 20 to 45 ⁇ m ⁇ g/cm 3 , from the viewpoint of composite yarn manageability and molded article strength.
  • the density D can be measured using a densitometer.
  • the monofilament diameter ( ⁇ m) can be calculated by the following formula:
  • Monofilament diameter 20 ⁇ fineness/( ⁇ number of filaments ⁇ density))
  • continuous reinforcing fibers may be used having the fineness (dtex) and number of filaments appropriately selected for the density of the continuous reinforcing fibers.
  • the density is about 2.5 g/cm 3 , and therefore a monofilament diameter of 2 to 40 ⁇ m may be selected. More specifically, when the monofilament diameter of the glass fiber is 9 ⁇ m, glass fibers with a fineness of 660 dtex and a filament number of 400 may be selected, for a product RD of 23.
  • the monofilament diameter of the glass fibers is 17 ⁇ m
  • glass fibers with a fineness of 11,500 dtex and a filament number of 2,000 may be selected, for a product RD of 43.
  • the density is about 1.8 g/cm 3 , and therefore a monofilament diameter of 2.8 to 55 ⁇ m may be selected.
  • carbon fibers with a fineness of 2,000 dtex and a filament number of 3,000 may be selected, for a product RD of 13.
  • the density is about 1.45 g/cm 3 , and therefore a monofilament diameter of 3.4 to 68 ⁇ m may be selected.
  • a monofilament diameter of the aramid fibers is 12 ⁇ m, aramid fibers with a fineness of 1,670 dtex and a filament number of 1,000 may be selected, for a product RD of 17.
  • Continuous reinforcing fibers such as glass fibers
  • the continuous reinforcing fibers may be in any form, but are preferably wound up into a yarn, cake or DWR for increased productivity and production stability in the resin-coating step. DWR is most preferred from the viewpoint of productivity.
  • the synthetic resin composing the matrix resin of the continuous fiber-reinforced molded resin of the embodiment may be a thermoplastic resin or a thermosetting resin, but it is preferably a thermoplastic resin from the viewpoint of the molding cycle and recycling properties.
  • thermoplastic resin composing the continuous fiber-reinforced molded resin of the embodiment may be of a single type or a combination of more than one type. It is preferred to use two or more thermoplastic resins from the viewpoint of adhesion with the continuous fiber-reinforced resin.
  • the proportion of the two or more thermoplastic resins that is occupied by resin other than the resin with the highest occupying proportion of the entire resin region is preferably higher than the proportion occupied by the resin with the highest occupying proportion of the entire resin region, from the viewpoint of productivity and of interfacial strength between the reinforcing fibers and the resin.
  • the thermoplastic resin has an absorption percentage of preferably 0.1 wt % or greater, more preferably 0.3 wt % or greater, even more preferably 0.5 wt % or greater, yet more preferably 0.8 wt % or greater, even yet more preferably 1.0 wt % or greater and most preferably 1.5 wt % or greater, from the viewpoint of reactivity between the coupling agent and the terminal functional groups of the thermoplastic resin.
  • the absorption percentage of the thermoplastic resin can be measured using a Karl Fischer moisture analyzer.
  • a catalyst that promotes reaction between the coupling agent and the terminal functional groups of the thermoplastic resin may also be added to the thermoplastic resin, and when glass fibers are selected as the continuous reinforcing fibers and a polyamide resin is selected as the thermoplastic resin, for example, examples of such a catalyst include phosphoric compounds such as sodium hypophosphite, which promote bonding reaction between the amino groups of the silane coupling agent and the terminal carboxyl groups of the polyamide resin.
  • the content of the particulate additive in the thermoplastic resin is preferably 30 ppm or lower, but from the viewpoint of mechanical strength of the continuous fiber-reinforced resin composite material it is more preferably 20 ppm or lower, even more preferably 10 ppm or lower and most preferably 5 ppm or lower.
  • thermoplastic resin An example for the particulate additive in the thermoplastic resin is carbon black.
  • the ⁇ -drop formation coefficient is an index of compatibility between the resin and reinforcing fibers, the ⁇ -drop formation coefficient affecting not only the main component of the resin but also affecting trace components in the resin.
  • the thermoplastic resin preferably has a ⁇ -drop formation coefficient of 10 or greater with the reinforcing fibers (assuming a number of touches of 4).
  • the ⁇ -drop formation coefficient can be calculated by the following formula, for example:
  • HM410 composite material boundary interface evaluator
  • the thermoplastic resin composing the matrix resin of the continuous fiber-reinforced molded resin of the embodiment may also consist of two or more types.
  • the resin with the highest occupying proportion of the entire resin region (the primary resin) preferably accounts for 85% to 99% of the total area occupied by the two or more thermoplastic resins, while the resin with the highest occupying proportion of the entire resin region (the primary resin) of the two or more thermoplastic resins is the resin with the highest melting point.
  • the difference between the melting point of the resin with the highest melting point and the melting point of the resin with the lowest melting point of the two or more thermoplastic resins is preferably 35° C. or higher, and more preferably 100° C. or higher.
  • the types of thermoplastic resins in the continuous fiber-reinforced molded resin can be identified by analyzing a cross-section of the continuous fiber-reinforced molded resin with a laser Raman microscope, and the melting point and glass transition temperature of each thermoplastic resin can be calculated from the composition of the resin, using a differential scanning calorimeter (DSC). From the viewpoint of heat resistance, the melting point of the thermoplastic resin mixture is preferably the same as the melting point of the resin with the highest occupying proportion of the entire resin region (the primary resin) in the thermoplastic resin.
  • the difference between the melting peak temperature during temperature increase and the crystallization peak temperature during temperature decrease for the mixture of the two or more thermoplastic resins forming the continuous fiber-reinforced molded resin of the embodiment is preferably smaller than the difference between the melting peak temperature during temperature increase and the crystallization peak temperature during temperature decrease of the resin with the highest occupying proportion of the entire resin region (primary resin), among the resins of the two or more thermoplastic resins, in order to obtain an excellent balance between moldability and impregnation rate.
  • the melting peak temperature during temperature increase and the crystallization peak temperature during temperature decrease can be calculated by DSC.
  • the bonding strength between at least one resin (secondary resin) other than the resin with the highest occupying proportion of the entire resin region (primary resin) and the continuous reinforcing fibers is preferably larger than the bonding strength between the resin with the highest occupying proportion of the entire resin region (primary resin) and the continuous reinforcing fibers, from the viewpoint of impregnating property and strength.
  • the bonding strength between each thermoplastic resin and the continuous reinforcing fibers can be determined by a push-out test using a nanoindenter.
  • the difference in surface tension between at least one resin (secondary resin) other than the resin with the highest occupying proportion of the entire resin region (primary resin) and the continuous reinforcing fibers is preferably larger than the difference in surface tension between the resin with the highest occupying proportion of the entire resin region (primary resin) and the continuous reinforcing fibers, from the viewpoint of impregnating property and strength.
  • the wettability of at least one resin (secondary resin) other than the resin with the highest occupying proportion of the entire resin region (primary resin) for the continuous reinforcing fibers is preferably greater than the wettability of the resin with the highest occupying proportion of the entire resin region (primary resin) for the continuous reinforcing fibers, from the viewpoint of impregnating property and strength.
  • the difference in surface tension and the wettability between each of the thermoplastic resins and the continuous reinforcing fibers can be evaluated by embedding a single continuous reinforcing fiber in the thermoplastic resin melted on a hot plate, and determining the length to which the thermoplastic resin is pulled on the continuous fiber when the continuous reinforcing fiber has been pulled.
  • the melt viscosity of the mixture of the two or more thermoplastic resins forming the continuous fiber-reinforced molded resin of the embodiment is preferably the same as the melt viscosity of the resin with the highest occupying proportion of the entire resin region (primary resin) of the two or more thermoplastic resins, for an excellent balance between strength and impregnating property.
  • the melt viscosity of the resin can be measured using a twin-capillary rheometer.
  • thermoplastic resins forming the continuous fiber-reinforced molded resin of the embodiment may be used in pre-compounded form, depending on the form of the intermediate material, or an intermediate material resin may be formed by dry blending.
  • thermoplastic resin is not particularly restricted, and it may be in the form of a film, pellets, fibers, a plate, powder or a reinforcing fiber coating.
  • thermoplastic resins include, but are not limited to, polyolefin-based resins such as polyethylene and polypropylene; polyamide-based resins such as polyamide 6, polyamide 66 and polyamide 46; polyester-based resins such as polyethylene terephthalate, polybutylene terephthalate and polytrimethylene terephthalate; polyacetal-based resins such as polyoxymethylene; polycarbonate-based resins; polyether-based resins such as polyether ketone, polyether ether ketone, polyether glycol, polypropylene glycol and polytetramethylene ether glycol; polyether sulfones; polyphenylene sulfides; thermoplastic polyetherimides; thermoplastic fluorine-based resins such as tetrafluoroethylene-ethylene copolymers; polyurethane-based resins; and acrylic-based resins, as well as modified thermoplastic resins obtained by modifying any of the foregoing.
  • polyolefin-based resins such as poly
  • thermoplastic resins polyolefin-based resins, polyamide-based resins, polyester-based resins, polyether-based resins, polyether sulfones, polyphenylene sulfides, thermoplastic polyetherimides and thermoplastic fluorine-based resins are preferred, with polyolefin-based resins, modified polyolefin-based resins, polyamide-based resins, polyester-based resins, polyurethane-based resins and acrylic-based resins being more preferred from the viewpoint of mechanical properties and general utility, and polyamide-based resins and polyester-based resins being even more preferred when the viewpoint of thermal properties is also considered. Polyamide-based resins are even more preferred from the viewpoint of durability against repeated load.
  • a polyester-based resin is a polymer compound having a —CO—O— (ester) bond in the main chain.
  • Polyester-based resins include, but are not limited to, polyethylene terephthalate, polybutylene terephthalate, polytetramethylene terephthalate, poly-1,4-cyclohexylenedimethylene terephthalate and polyethylene-2,6-naphthalene dicarboxylate.
  • a polyester-based resin may be a homopolyester or a copolymerized polyester.
  • a suitable third component is preferably copolymerized with a homopolyester, where examples for the third component include, but are not limited to, diol components such as diethylene glycol, neopentyl glycol and polyalkylene glycol, and dicarboxylic acid components such as adipic acid, sebacic acid, phthalic acid, isophthalic acid and 5-sodiumsulfoisophthalic acid.
  • diol components such as diethylene glycol, neopentyl glycol and polyalkylene glycol
  • dicarboxylic acid components such as adipic acid, sebacic acid, phthalic acid, isophthalic acid and 5-sodiumsulfoisophthalic acid.
  • a polyester-based resin employing a biomass resource-derived starting material may also be used, where examples include, but are not limited to, aliphatic polyester-based resins such as polylactic acid, polybutylene succinate and polybutylene succinate adipate, and aromatic polyester-based resins such as polybutylene adipate terephthalate.
  • a polyamide-based resin is a polymer compound having a —CO—NH— (amide) bond in the main chain.
  • Examples includes aliphatic polyamides, aromatic polyamides and fully aromatic polyamides, with aliphatic polyamides being preferred from the viewpoint of high affinity with the reinforcing fibers and more easily obtaining a reinforcing effect with the reinforcing fibers.
  • the amount of carboxyl terminal groups in the polyamide resin is preferably 65 ⁇ mol/g or greater from the viewpoint of adhesion between the resin and the reinforcing fibers, and it is more preferably 70 ⁇ mol/g or greater, even more preferably 75 ⁇ mol/g or greater and yet more preferably 80 ⁇ mol/g or greater.
  • the amount of amino terminal groups in the polyamide resin is preferably 40 ⁇ mol/g or less from the viewpoint of adhesion between the resin and the reinforcing fibers, and it is more preferably 35 ⁇ mol/g or less, even more preferably 30 ⁇ mol/g or less and yet more preferably 25 ⁇ mol/g or less.
  • polyamide-based resins include, but are not limited to, polyamides obtained by ring-opening polymerization of lactams, polyamides obtained by self-condensation of ⁇ -aminocarboxylic acids, polyamides obtained by condensation of diamines and dicarboxylic acids, and copolymers of the foregoing.
  • Such polyamide-based resins may be used alone, or two or more may be used in admixture.
  • lactams include, but are not limited to, pyrrolidone, caprolactam, undecanelactam and dodecalactam.
  • ⁇ -aminocarboxylic acids include, but are not limited to, ⁇ -amino fatty acids that are lactam compounds having the rings opened with water. Two or more different lactam or ⁇ -aminocarboxylic acid monomers may also be condensed together.
  • diamines examples include, but are not limited to, straight-chain aliphatic diamines such as hexamethylenediamine or pentamethylenediamine; branched aliphatic diamines such as 2-methylpentanediamine or 2-ethylhexamethylenediamine; aromatic diamines such as p-phenylenediamine or m-phenylenediamine; and alicyclic diamines such as cyclohexanediamine, cyclopentanediamine or cyclooctanediamine.
  • straight-chain aliphatic diamines such as hexamethylenediamine or pentamethylenediamine
  • branched aliphatic diamines such as 2-methylpentanediamine or 2-ethylhexamethylenediamine
  • aromatic diamines such as p-phenylenediamine or m-phenylenediamine
  • alicyclic diamines such as cyclohexanediamine, cyclopentanedia
  • dicarboxylic acids examples include, but are not limited to, aliphatic dicarboxylic acids such as adipic acid, pimelic acid and sebacic acid; aromatic dicarboxylic acids such as phthalic acid and isophthalic acid; and alicyclic dicarboxylic acids such as cyclohexanedicarboxylic acid.
  • a diamine and dicarboxylic acid as monomers may be condensed with either one each alone, or two or more in combination.
  • polyamide-based resins include, but are not limited to, polyamide 4 (poly ⁇ -pyrrolidone), polyamide 6 (polycaproamide), polyamide 11 (polyundecaneamide), polyamide 12 (polydodecaneamide), polyamide 46 (polytetramethylene adipamide), polyamide 66 (polyhexamethylene adipamide), polyamide 610, polyamide 612, polyamide 6T (polyhexamethylene terephthalamide), polyamide 9T (polynonanemethylene terephthalamide) and polyamide 6I (polyhexamethylene isophthalamide), as well as copolymerized polyamides containing these as constituent components.
  • polyamide 4 poly ⁇ -pyrrolidone
  • polyamide 6 polycaproamide
  • polyamide 11 polyundecaneamide
  • polyamide 12 polydodecaneamide
  • polyamide 46 polytetramethylene adipamide
  • polyamide 66 polyhexamethylene adipamide
  • copolymerized polyamides include, but are not limited to, copolymers of hexamethylene adipamide and hexamethylene terephthalamide, copolymers of hexamethylene adipamide and hexamethylene isophthalamide, and copolymers of hexamethylene terephthalamide and 2-methylpentanediamine terephthalamide.
  • a shaped molded article can be produced from the fiber-reinforced composite material by a method including a step in which the continuous fiber-reinforced resin composite material produced by the method described above is heated at above the melting point of the thermoplastic resin using an IR heater, for example, and pressed using a die, and then cooled to a temperature below the melting point of the thermoplastic resin and shaped.
  • thermosetting resins include, but are not limited to, epoxy resins, phenol resins, melamine resins, urea resins and unsaturated polyester resins. These thermosetting resins may be used alone or in combinations of two or more.
  • the continuous fiber-reinforced molded resin of the embodiment can be suitably used in structural materials for aircraft, vehicles, construction materials, robots and communication device housings.
  • Examples of uses for vehicles include, but are not limited to, chassis/frames, suspensions, drive system components, interior parts, exterior parts, functional parts and other parts.
  • suitable uses include use in a part for a steering axis, mount, sunroof, step, roof trimming, door trimming, trunk, boot lid, bonnet, sheet frame, sheet back, retractor, retractor support bracket, clutch, gear, pulley, cam, auger, elasticity beam, buff ring, lamp, reflector, glazing, front-end module, back door inner, brake pedal, handle, electrical material, sound-absorbing material, door exterior, interior finishing panel, instrument panel, rear gate, ceiling cover, sheet, seat framework, wiper strut, EPS (Electric Power Steering), small motor, heat sink, ECU (Engine Control Unit) box, ECU housing, steering gear box housing, plastic housing, EV (Electric Vehicle) motor housing, wire harness, in-vehicle meter, combination switch, small motor, spring, damper, wheel, wheel cover, frame, sub-frame, side frame, motorcycle frame, fuel tank, oil pan, intake manifold, propeller shaft, driving motor, monocoque, hydrogen tank, fuel cell electrode, panel, floor panel, outer
  • the continuous fiber-reinforced molded resin of the embodiment may be in a rectangular solid shape, for example, for communication device housing purposes.
  • the properties of a housing is an electric field shielding property of preferably lower than 10 dB, more preferably lower than 5 dB and even more preferably lower than 0.1 dB in the frequency band of 1 GHz, as measured by the KEC method.
  • Continuous tempered glass fibers may be used as the continuous reinforcing fibers with this property.
  • the average wall thickness of the housing is preferably 1 mm or smaller, more preferably 0.5 mm or smaller and most preferably 0.4 mm or smaller.
  • a housing of the desired thickness, having low disorder of the continuous fibers and no generation of voids, can be produced via a preform.
  • the continuous fiber-reinforced molded resin was cut with a band saw, and the cut test piece was polished using a polishing machine (IS-POLISHER ISPP-1000 compact precision material fabrication system (Ikegami Seiki Co., Ltd.)), with a pressure of 400 g/cm 2 on the polishing surface.
  • a polishing machine IS-POLISHER ISPP-1000 compact precision material fabrication system (Ikegami Seiki Co., Ltd.)
  • the polishing was carried out for 10 minutes with #220 waterproof paper, 2 minutes with #400 waterproof paper, 5 minutes with #800 waterproof paper, 10 minutes with #1200 waterproof paper, 15 minutes with #2000 waterproof paper, 15 minutes with 9 ⁇ m silicon carbide film particles, 15 minutes with 5 ⁇ m alumina film particles, 15 minutes with 3 ⁇ m alumina film particles, 15 minutes with 1 ⁇ m alumina film particles, and 10 minutes with 0.1 ⁇ m colloidal silica particles (BAIKALOX 0.1CR) with buffing paper foamed polyurethane, at approximately 7 mL/min while adding water.
  • BAIKALOX 0.1CR colloidal silica particles
  • the polished sample was observed with an SEM (S-4700, by Hitachi High-Technologies Corp.), and the void percentage in the region of 1/10 of the radius of the single continuous reinforcing fiber was calculated from the obtained image.
  • SEM S-4700, by Hitachi High-Technologies Corp.
  • Impregnation rate (%) ⁇ 1 ⁇ (void area/continuous reinforcing fiber bundle area) ⁇ 100.
  • a test strip with a length of 70 mm, a width of 10 mm and a wall thickness of 2 mm was cut out from the molded article, and the tensile stress (MPa) of the test piece was measured using an Instron universal testing machine at a speed of 5 mm/min, with chucking at a spacing of 30 mm in the lengthwise direction, in a thermostatic bath with an environment of 23° C., 50% RH, and 150° C., 50%.
  • MPa flexural stress
  • GPa flexural modulus
  • a 2 g portion was cut out of the continuous fiber-reinforced molded resin, and was placed in an electric furnace and heated at 650° C. for 3 hours to burn off the resin. It was then allowed to naturally cool to room temperature, and the mass of the remaining glass fibers was measured to determine the proportion of glass fibers and resin in the continuous fiber-reinforced molded resin. Using the calculated proportion, it was divided by the density to determine the volume ratio (Vf) of reinforcing fibers with respect to the continuous fiber-reinforced molded resin. The amount of resin leaked during molding was determined from the amount of charged resin and the amount of resin in the continuous fiber-reinforced molded resin after molding, and the amount of leaked resin was divided by the amount of charged resin to calculate the quantity ratio of leaked resin.
  • Vf volume ratio
  • a cross-section of the continuous fiber-reinforced molded resin in the thickness direction was cut out at each of 5 arbitrary locations, embedded in an epoxy resin, and polished while taking care that the continuous reinforcing fibers were not damaged.
  • a mapping image of the cross-section was taken using a laser Raman microscope (inViaQontor confocal Raman microscope, product of Renishaw Co.), and the types of resins of the fiber-reinforced resins were identified from the obtained image and spectrum.
  • Each area was also calculated by image processing using ImageJ, and the occupying ratio of the resin in the region of 1/10 of the radius of a single continuous reinforcing fiber from the edge of the single continuous reinforcing fiber (the area ratio) was calculated.
  • the area ratio for each resin occupying the region of 1/10 of the radius of the single continuous reinforcing fiber was calculated for 10 arbitrary continuous reinforcing fibers in the cross-section, and the average was calculated.
  • the continuous fiber-reinforced molded resin was polished with a polishing machine (IS-POLISHER ISPP-1000 compact precision material fabrication system, Ikegami Seiki Co., Ltd.), with a force of 125 g/cm 2 on the polished surface.
  • a polishing machine IS-POLISHER ISPP-1000 compact precision material fabrication system, Ikegami Seiki Co., Ltd.
  • the polishing was carried out for 10 minutes with #220 waterproof paper, 10 minutes with #1200 waterproof paper, 5 minutes with #2000 waterproof paper, 10 minutes with 9 ⁇ m silicon carbide film particles, 10 minutes with 5 ⁇ m alumina film particles, 5 minutes with 3 ⁇ m alumina film particles, 5 minutes with 1 ⁇ m alumina film particles, and 5 minutes with 0.1 ⁇ m colloidal silica particles (BAIKALOX 0.1CR) with buffing paper foamed polyurethane, at approximately 7 mL/min while adding water.
  • the polished sample was subjected to electron staining by immersion for 18 hours in a 5 wt % aqueous solution of 12 tungsten(VI) phosphate n-hydrate, while taking care not to allow collapse of the polished surface.
  • thermoplastic resin After drying, the distribution of the thermoplastic resin at 50 ⁇ m ⁇ 50 ⁇ m portions at 5 arbitrary locations was observed using a SEM (S-4700, Hitachi High-Technologies Corp.), and the area of each was calculated by image processing using imageJ. Based on the distribution it was assessed whether each specific resin was evenly dispersed or mixed in the resin regions other than the interface region.
  • a continuous fiber-reinforced molded resin with a 2 mm thickness was cut with a band saw to a width of 5 mm and a length of 60 mm in the 0° and 90° directions with respect to the fiber direction, and a dynamic viscoelasticity measuring apparatus (AresG2, TA Instruments) was used for measurement, under a nitrogen atmosphere, in a measuring temperature range of 30° C. to 250° C. at a temperature-elevating rate of 5.0° C./min, with an angular frequency of 10 rad/s and with the deformation mode in twisting mode.
  • the value of the loss tangent and its temperature were obtained from the peak top value of the graph plotting the loss tangent at each temperature, and from its associated temperature. The value of the loss tangent was used as the peak top at the low-temperature end.
  • a graph of test force with respect to displacement was drawn, and the integral value until maximum impact force was reached was calculated, recording the average value of 5 samples as the shock absorption energy.
  • a continuous fiber-reinforced molded resin with a 2 mm thickness was cut with a band saw to a width of 5 mm and a length of 60 mm in the 0° and 90° directions or in a 45° direction (diagonal direction) with respect to the fiber direction, and a dynamic viscoelasticity measuring apparatus (AresG2, TA Instruments) was used for measurement, under a nitrogen atmosphere, in a measuring temperature range of 30° C. to 250° C. at a temperature-elevating rate of 5.0° C./min, with an angular frequency of 10 rad/s and with the deformation mode in twisting mode.
  • the value of the storage modulus and its temperature were obtained from the peak top value of the graph plotting the storage modulus at each temperature, and from its associated temperature.
  • a graph of test force with respect to displacement was drawn, and the maximum impact strength was calculated as the average value of 5 samples.
  • a continuous fiber-reinforced molded resin with a 2 mm thickness was cut with a band saw to a width of 5 mm and a length of 60 mm in the 0° and 90° directions or in a 45° direction (diagonal direction) with respect to the fiber direction, and a dynamic viscoelasticity measuring apparatus (EPLEXOR-SOON, ITS Japan, Inc.) was used for measurement, under a nitrogen atmosphere, in a measuring temperature range of 25° C. to 250° C. at a temperature-elevating rate of 3.0° C./min, with an oscillation frequency of 8 Hz and with the deformation mode in bending mode, recording the maximum value as the bending storage modulus.
  • the storage modulus was obtained at different temperatures.
  • a continuous fiber-reinforced molded resin with a 2 mm thickness was cut with a band saw to a width of 5 mm and a length of 60 mm in the 0° and 90° directions with respect to the fiber direction, and a dynamic viscoelasticity measuring apparatus (EPLEXOR-SOON, ITS Japan, Inc.) was used for measurement, under a nitrogen atmosphere, in a measuring temperature range of 20° C. to 250° C. at a temperature-elevating rate of 3.0° C./min, with an oscillation frequency of 8 Hz and with the deformation mode in tension mode, obtaining the storage modulus at different temperatures. The maximum value between 20° C. and 200° C. in the plot of the loss tangent at different temperatures was recorded as the tensile loss tangent.
  • thermoplastic resins Using a DSC-60 by Shimadzu Corp., with a sample amount of approximately 5 mg, a mixture of two or more thermoplastic resins, or each one separately, was heated with atmospheric gas flowing at 30 mL/min and temperature increase of 10° C./min, from room temperature (25° C.) to above the expected melting point, to melting, after which the molten polyamide resin was cooled at 10° C./min, and the crystallization temperature was recorded as the peak top temperature among the observed exothermic peaks. Next, the temperature was raised again at a speed of 10° C./min to above the melting point, and the melting point was recorded as the peak top among the observed endothermic peaks.
  • the continuous fiber-reinforced molded resin was cut to a thickness of 30 ⁇ m as a cross-section perpendicular to the lengthwise direction of the continuous reinforcing fibers, and polished while taking care that the continuous reinforcing fibers were not damaged. Using the polished sample, the reinforcing fibers were extruded out using a nanoindenter (iMicro, Nanomechenics, Inc.) to measure the bonding strength between the reinforcing fibers and the thermoplastic resin.
  • a nanoindenter iMicro, Nanomechenics, Inc.
  • the assessment was “G” when the bonding strength between the reinforcing fibers and the resin (secondary resin) other than the resin with the highest occupying proportion of the entire resin region (primary resin), among the thermoplastic resins, was stronger than the bonding strength between the reinforcing fibers and the resin with the highest occupying proportion of the entire resin region (primary resin), and “P” when it was weaker.
  • thermoplastic resin melted on a hot plate that had been heated to 280° C.
  • a 1 mm continuous reinforcing fiber was pulled at 1 mm/sec while observing it under a microscope, and the length to which the thermoplastic resin was pulled by the continuous fiber during that time was assessed.
  • the wettability and surface tension were assessed as “G” when the length to which the resin (secondary resin) other than the resin with the highest occupying proportion of the entire resin region (primary resin), among the thermoplastic resins, was pulled by the reinforcing fibers was greater than the length to which the resin with the highest occupying proportion of the entire resin region (primary resin), among the thermoplastic resins, was pulled by the reinforcing fibers, and “P” when it was less.
  • Measurement was performed using a twin-capillary rheometer (Rosand Precision) at 280° C., varying the shear rate to 100/s, 200/s, 400/s, 1000/s, 2000/s, 4000/s and 8000/s.
  • Rosand Precision a twin-capillary rheometer
  • For a shear rate of 4000/s an assessment of “G” was assigned when the melt viscosity of the mixture of two or more thermoplastic resins was 4/5 to 5/4 times the viscosity of the resin with the highest occupying proportion of the entire resin region, among the two or more thermoplastic resins, and an assessment of “P” was assigned otherwise.
  • a Karl Fischer moisture analyzer (MKC610 by Kyoto Electronics Co., Ltd.) was used to weigh out and measure 0.3 g of thermoplastic resin under a nitrogen atmosphere.
  • a 2 g portion was cut out of the continuous fiber-reinforced resin composite material, and was placed in an electric furnace and heated at 650° C. for 3 hours to burn off the resin. It was then allowed to naturally cool to room temperature, and the mass of the remaining glass fibers was measured to determine the proportion of glass fibers and resin in the continuous fiber-reinforced resin composite material. Using the calculated proportion, it was divided by the density to determine the volume ratio (Vf) of reinforcing fibers with respect to the continuous fiber-reinforced resin composite material.
  • Vf volume ratio
  • the undissolved portion was washed twice with HFIP and vacuum dried, and then an XPS (VersaProbe II, product of Ulvac-Phi, Inc.) was used for measurement with an excitation source of mono.AlK ⁇ 20 kV ⁇ 5 mA 100 W, an analysis size of 100 ⁇ m ⁇ 1.4 mm, and with a photoelectron take-off angle.
  • XPS VeryProbe II, product of Ulvac-Phi, Inc.
  • Acoustic emission measurement was carried out using a continuous fiber-reinforced resin composite material cut out to a thickness of 2.0 mm, a length of 14 mm (7 ⁇ the thickness) and a width of 10 mm, in an interlaminar shear test (JIS K7078) in which an AE sensor (AE-900 M) was mounted, with 10 mm between spans (5 ⁇ the thickness) and with the test speed set to 1 mm/min.
  • JIS K7078 interlaminar shear test
  • AE-900 M AE sensor
  • Analysis was performed with the preamp set to 34 dB, the threshold value to 30 dB and the filter to 95 kHz-960 kHz, defining an AE signal with an AE amplitude of lower than 50 dB and an AE signal duration of shorter than 1000 ⁇ s as corresponding to resin damage, an AE signal with an AE amplitude of 60 dB or higher and an AE signal duration of 1000 ⁇ s or longer as corresponding to interlayer separation, and an AE signal with an AE amplitude of 50 dB or higher and an AE signal duration of shorter than 1000 ⁇ s as corresponding to glass fiber damage.
  • the ⁇ -drop formation coefficient was measured using a composite material boundary interface property evaluator (HM410 by Toei Sangyo Co., Ltd.), with the resin set in the heating furnace unit and the furnace temperature set to 40° C. below the melting point of the resin, adhering the resin to each of the individual reinforcing fibers set in the evaluator.
  • HM410 composite material boundary interface property evaluator
  • the furnace temperature was increased 10° C. at a time until the resin melted to adhere the resin onto the reinforcing fiber.
  • the resin fused onto the reinforcing fiber was touched 4 times to adhere the resin and then allowed to stand for 1 minute, the number of ⁇ -drops generated was counted, and calculation was performed using the following formula:
  • a tensile impact dumbbell TypeS test piece conforming to ASTM-D1822 was prepared, and the test was conducted with an EHF-EB50kN-40L (RV) (product of Shimadzu Corp.), using a testing temperature of 23° C., a frequency of 20 Hz, a sine wave waveform, a chuck distance of 35 mm and a minimum load set to 10% load.
  • EHF-EB50kN-40L RV
  • Glass fibers were produced in a filament number of 2000, with a fineness of 11,500 dtex and with 0.45 mass % adhesion of the sizing agent.
  • the winding form was DWR and the mean monofilament diameter was 17 ⁇ m.
  • the glass fiber sizing agent was produced by copolymerizing 0.5 mass % of ⁇ -aminopropyltriethoxysilane (aminosilane) KBE-903 (product of Shin-Etsu Chemical Co., Ltd.), 1 mass % of carnauba wax, 2 mass % of polyurethane resin Y65-55 (product of Adeka Corp.), 40 mass % of maleic anhydride, 50 mass % of methyl acrylate and 10 mass % of methyl methacrylate, and using deionized water for adjustment to 3 mass % of a copolymer compound with a weight-average molecular weight of 20,000 and 3 mass % of the copolymer compound aqueous solution.
  • Glass fibers were produced in the same manner as glass fibers (A), except for using a fineness of 2900 dtex, a filament number of 800 and a mean monofilament diameter of 13 ⁇ m.
  • Polyamide resin A Polyamide 66 (LEONA 1300S (Asahi Kasei Corp.)), having a melting point of 265° C., a difference between melting peak temperature and crystallization peak temperature during temperature decrease (Tm ⁇ Tc) of 53° C., a number of carboxyl terminal groups of 70 ⁇ mol/g and an amino terminal group content of 32 ⁇ mol/g (Example 6-).
  • Polyamide resin B Polyamide 6/12 (GRILON C CF6S (EMS-Chemie, Japan), melting point: 130° C.
  • Polyamide resin C Polyamide 66 (LEONA 1402S (Asahi Kasei Corp.))
  • Polyamide 6 (Examples 4-, 5-): GRILON BS/2 Natural (EMS-Chemie, Japan), melting point: 225° C.
  • Polyamide 6I (Example 5-): LEONA R16024 (Asahi Kasei Corp.), glass transition temperature: 130° C.
  • Polyamide 6T/6I (Example 5-): Trial product by Toyobo, Ltd.
  • PE Polyethylene
  • Example 5- SANTECH J240 (Asahi Kasei Corp.), melting point: 125° C.
  • thermoplastic resins A and/or B were molded with a T-die extruder (product of Soken Co., Ltd.) to obtain a film.
  • the thickness of the film was 100 ⁇ m.
  • a rapier loom (weaving width: 2 m) was used for weaving using the glass fibers as the warp yarn and weft yarn, to produce a glass cloth.
  • the woven form of the obtained glass cloth was a plain weave, the woven density was 6.5/25 mm and the basis weight was 600 g/m 2 .
  • Glass cloth (Example 5-): WFR 350 100BS6 (Nittobo Co., Ltd.)
  • Carbon fiber fabric (Example 5-): Carbon fibers in a filament number of 12,000 with a fineness of 8000 dtex, and having polyvinylpyrrolidone adhering at 2.8 mass %, were produced and used for weaving (plain weaving) with a rapier loom.
  • a master batch containing carbon black (Asahi Kasei Corp.) was used as a particulate additive.
  • the carbon black content was 3 wt %.
  • the molding machine used was a hydraulic molding machine (Shoji Co.) with a maximum mold clamping force of 50 tons.
  • a die with an inlay structure was prepared to obtain a flat continuous fiber-reinforced molded resin (200 mm length, 100 mm width, 2 mm wall thickness).
  • the glass cloth and polyamide film were cut to the die shape, layered in the prescribed number, and set in the die.
  • the internal temperature of the molding machine was raised to 330° C., and then the mold was clamped with a mold clamping force of 5 MPa for compression molding.
  • the molding time was 1 minute after reaching 265° C. as the melting point of polyamide 66, and after quenching of the die, it was released and the molded article was removed.
  • the maximum temperature during molding was 275° C.
  • a double belt press apparatus (process system) was used as the molding machine. Five glass cloths and 10 polyamide films were fed out from rolls. The device heater temperature was 330° C., and cooling was by water-cooling. Pressurization was at a pressure of 30 kN, and transport was at 0.2 m/min.
  • the molding time was 1 minute after reaching 265° C. as the melting point of polyamide 66, and after quenching of the die, it was released and the molded article was removed.
  • the maximum temperature during molding was 285° C.
  • the temperature in the molding machine was set to 300° C.
  • the molding time was 15 minutes after reaching 265° C. as the melting point of polyamide 66, and after quenching of the die, it was released and the molded article was removed.
  • the maximum temperature during molding was 300° C.
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 1-1, except that molding was for 30 seconds after reaching 265° C. The maximum temperature during molding was 280° C.
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 1-2, except that an epoxy resin was used instead of the polyamide resin A film.
  • a glass cloth was produced using the glass fibers, after adhering 0.3 mass % of 3-glycidoxypropyltrimethoxysilane (KBM-402, Shin-Etsu Chemical Co., Ltd.), 1.5 mass % of an epoxy resin emulsion and 0.2 mass % of carnauba wax, as the sizing agent.
  • Six of the glass cloths were layered and set in a die, 16 g of a bisphenol A-type liquid epoxy resin (jER828 by Mitsubishi Chemical Corp.) and 1.6 g of bisphenol A (4,4′-(propane-2,2-diyl)diphenol were loaded in, and the temperature inside the molding machine was set to 40° C. for compression molding for 3 days at a mold clamping pressure of 5 MPa, to obtain a continuous fiber-reinforced molded resin.
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 1-1, except that the number of glass cloths was 5, and the number of polyamide resin A films was 10.
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 1-1, except that glass fibers without addition of a sizing agent were used.
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 1-1, except that the glass fibers used were adhered with a sizing agent that was 0.3 mass % of 3-glycidoxypropyltrimethoxysilane as a silane coupling agent, 1.5 mass % of an epoxy resin emulsion and 0.2 mass % of carnauba wax.
  • Example 1-1 Evaluation was conducted in the same manner as Example 1-1, for “Tepex Dynalite 101” by Bond Laminate Co. comprising a glass cloth impregnated with polyamide 66.
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 1-2, except that molding was with the internal temperature of the molding machine set to 265° C. The maximum temperature during molding was 265° C.
  • Example 1-1 0.5 87 649 950 36 100 65 0.1 Example 1-2 0.2 91 654 960 40 100 65 0.3 Example 1-3 2 60 620 850 33 99 65 0.1 Example 1-4 0.1 98 680 970 44 100 65 0.1 Example 1-5 4 30 580 830 30 98 65 0.1 Example 1-6 0.5 90 580 930 30 100 50 0.1 Comparative 50 2 180 300 12 85 65 0.1 Example 1-1 Comparative 30 5 350 400 18 90 65 0.1 Example 1-2 Comparative 25 8 380 560 23 100 47 Example 1-3 Comparative 30 8 440 530 23 97 65 0.3 Example 1-6
  • the continuous fiber-reinforced molded resins of Examples 1-1 to 1-6 exhibited very high tensile stress, flexural stress and flexural moduli, because they were continuous fiber-reinforced resins in which at least 10% had a void percentage in the region of 1/10 of the radius of a single continuous reinforcing fiber from the edge of the single continuous reinforcing fiber that was 10% or lower. Their physical properties were much more satisfactory than the physical properties of a molded article obtained using the commercially available intermediate material of Comparative Example 1-3.
  • the molding time was 1 minute after reaching 265° C. as the melting point of polyamide 66, and after quenching of the die, it was released and the molded article was removed.
  • the maximum temperature during molding was 285° C.
  • the temperature in the molding machine was set to 300° C.
  • the molding time was 10 minutes after reaching 265° C. as the melting point of polyamide 66, and after quenching of the die, it was released and the molded article was removed.
  • the maximum temperature during molding was 300° C.
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 2-1, except that molding was for 30 seconds after reaching 265° C. The maximum temperature during molding was 280° C.
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 2-1, except that the polyamide film was a film of polyamide resin B.
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 2-1, except that the number of glass cloths was 5, and the number of polyamide resin A films was 10.
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 2-2, except that the number of glass cloths was 5, and the number of polyamide resin A films was 10.
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 2-1, except that glass fibers without addition of a sizing agent were used.
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 2-6, except that the glass fibers used were adhered with a sizing agent that was 0.3 mass % of 3-glycidoxypropyltrimethoxysilane as a silane coupling agent, 1.5 mass % of an epoxy resin emulsion and 0.2 mass % of carnauba wax.
  • Example 2-1 Evaluation was conducted in the same manner as Example 2-1, for “Tepex Dynalite 101” by Bond Laminate Co. comprising a glass cloth impregnated with polyamide 66.
  • the continuous fiber-reinforced molded resins of Examples 2-1 to 2-6 exhibited very high shock absorption energy, because the loss tangent in twisting mode was 0.11 or lower. Their physical properties were much more satisfactory than the physical properties of a molded article obtained using the commercially available intermediate material of Comparative Example 2-3.
  • the molding time was 1 minute after reaching 265° C. as the melting point of polyamide 66, and after quenching of the die, it was released and the molded article was removed.
  • the maximum temperature during molding was 285° C.
  • the temperature in the molding machine was set to 300° C.
  • the molding time was 10 minutes after reaching 265° C. as the melting point of polyamide 66, and after quenching of the die, it was released and the molded article was removed.
  • the maximum temperature during molding was 300° C.
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 3-1, except that molding was for 30 seconds after reaching 265° C. The maximum temperature during molding was 280° C.
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 3-1, except that the polyamide film was a film of polyamide resin B.
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 3-1, except that the number of glass cloths was 5, and the number of polyamide resin A films was 10.
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 3-2, except that the number of glass cloths was 5, and the number of polyamide resin A films was 10.
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 3-1, except that glass fibers without addition of a sizing agent were used.
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 3-6, except that the glass fibers used were adhered with a sizing agent that was 0.3 mass % of 3-glycidoxypropyltrimethoxysilane as a silane coupling agent, 1.5 mass % of an epoxy resin emulsion and 0.2 mass % of carnauba wax.
  • Example 3-1 Evaluation was conducted in the same manner as Example 3-1, for “Tepex Dynalite 101” by Bond Laminate Co. comprising a glass cloth impregnated with polyamide 66.
  • the continuous fiber-reinforced molded resins of Examples 3-1 to 3-6 exhibited very high impact strength, because the storage modulus in twisting mode was 3.4 GPa or greater. Their physical properties were much more satisfactory than the physical properties of a molded article obtained using the commercially available intermediate material of Comparative Example 3-3.
  • the temperature in the molding machine was set to 300° C.
  • the molding time was 10 minutes after reaching 265° C. as the melting point of polyamide 66, and after quenching of the die, it was released and the molded article was removed.
  • the maximum temperature during molding was 300° C.
  • the bending storage modulus at this time was 31 GPa
  • the bending storage modulus at 150° C. was 24 GPa (retention: 77%)
  • the bending storage modulus when cut diagonally was 20 GPa (retention: 64%)
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 4-2, except that molding was for 30 seconds after reaching 265° C.
  • the maximum temperature during molding was 280° C.
  • the bending storage modulus at this time was 28 GPa, and the impact strength was 8.81 kN.
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 4-2, except that the polyamide film was a film of polyamide resin B.
  • the bending storage modulus at this time was 33 GPa, and the impact strength was 9.05 kN.
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 4-1, except that molding was for 1 minute after reaching 265° C.
  • the maximum temperature during molding was 285° C.
  • the bending storage modulus at this time was 31 GPa, and the impact strength was 8.50 kN.
  • the molding time was 1 minute after reaching 265° C. as the melting point of polyamide 66, and after quenching of the die, it was released and the molded article was removed.
  • the maximum temperature during molding was 285° C.
  • the bending storage modulus at this time was 36 GPa, and the impact strength was 9.10 kN.
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 6, except that glass fibers without addition of a sizing agent were used.
  • the bending storage modulus at this time was 15 GPa, and the impact strength was 3.20 kN.
  • a continuous fiber-reinforced molded resin was obtained in the same manner as Example 4-1, except that the glass fibers used were adhered with a sizing agent that was 0.3 mass % of 3-glycidoxypropyltrimethoxysilane as a silane coupling agent, 1.5 mass % of an epoxy resin emulsion and 0.2 mass % of carnauba wax.
  • the bending storage modulus at this time was 20 GPa, and the impact strength was 5.21 kN.
  • Example 4-1 Evaluation was conducted in the same manner as Example 4-1, for “Tepex Dynalite 101” by Bond Laminate Co. comprising a glass cloth impregnated with polyamide 66.
  • the bending storage modulus at this time was 20.8 GPa
  • the bending storage modulus at 150° C. was 15.7 GPa (retention: 75%)
  • the bending storage modulus when cut diagonally was 11.9 GPa (retention: 57%)
  • the continuous fiber-reinforced molded resins of Examples 4-1 to 4-6 exhibited very high impact strength, because the bending storage modulus in twisting mode was 22 GPa or greater. Their physical properties were much more satisfactory than the physical properties of a molded article obtained using the commercially available intermediate material of Comparative Example 4-3.
  • thermoplastic resin film was produced using a dry blend of PA66 and PA6/12 in a weight ratio of 8:1. The thickness of the film was 100 ⁇ m. After alternately laminating 11 films and 10 glass cloths, they were molded. The PA6/12 was evenly dispersed in the PA66 in the resin region other than the interface region with the glass fibers.
  • a continuous fiber-reinforced molded resin was produced in the same manner as Example 5-1, except for using PA6 instead of PA6/12.
  • the PA6 was evenly dispersed in the PA66 in the resin region other than the interface region with the glass fibers.
  • a continuous fiber-reinforced molded resin was produced in the same manner as Example 5-1, except for using PE instead of PA6/12.
  • the PE was evenly dispersed in the PA66 in the resin region other than the interface region with the glass fibers.
  • a continuous fiber-reinforced molded resin was produced in the same manner as Example 5-1, except for using PA6I instead of PA6/12.
  • the PA6I was evenly dispersed in the PA66 in the resin region other than the interface region with the glass fibers.
  • a continuous fiber-reinforced molded resin was produced in the same manner as Example 5-1, except that PA66 and PA6/12 were dry blended in a weight ratio of 5:4.
  • the PA6/12 was evenly dispersed in the PA66 in the resin region other than the interface region with the glass fibers.
  • thermoplastic resin film was produced using a mixture of PA66 and PA6/12 prekneaded with a charging ratio (weight ratio) of 8:1 using a twin-screw extruder (TEM26SS, Toshiba Machine Co., Ltd.).
  • the PA6/12 was evenly dispersed in the PA66 in the resin region other than the interface region with the glass fibers.
  • a continuous fiber-reinforced molded resin was produced in the same manner as Example 5-1, except that a carbon fiber fabric was used instead of a glass cloth.
  • the PA6/12 was evenly dispersed in the PA66 in the resin region other than the interface region with the glass fibers.
  • a continuous fiber-reinforced molded resin was produced in the same manner as Example 5-1, except that the film was produced using PA66 alone.
  • a continuous fiber-reinforced molded resin was produced in the same manner as Example 5-1, except for using PA6T/6I instead of PA6/12.
  • the PA6T/6I was evenly dispersed in the PA66 both in the resin region other than the interface region with the glass fibers, and in the interface region.
  • a glass cloth was cut out to 19.5 cm ⁇ 9.5 cm and immersed in a solution of a polyamide emulsion adjusted to 30 mass % with purified water (SEPOLSION PA200 by Sumitomo Seika Chemicals Co., Ltd.), after which it was dried at 80° C. for 1 hour with a hot air circulation dryer to prepare a composite material.
  • the coverage of the PA6/12 polyamide emulsion solid component on the glass cloth in the obtained composite material was 6 mass %.
  • a continuous fiber-reinforced molded resin was produced in the same manner as Example 5-1, except that PA66 and PA6/12 were dry blended in a weight ratio of 1:8.
  • the PA66 was evenly dispersed in the PA6/12 in the resin region other than the interface region with the glass fibers.
  • FIG. 3 shows a photograph of an interface region in the obtained molded article.
  • the molding time was 1 minute after reaching 265° C. as the melting point of polyamide 66, and after quenching of the die, it was released and the molded article was removed.
  • the maximum temperature during molding was 285° C.
  • the absorption percentage of the polyamide resin was 0.2 wt %.
  • a continuous fiber-reinforced resin composite material was obtained in the same manner as Example 6-1, except that the polyamide resin film was dried with a vacuum dryer before molding.
  • the absorption percentage of the polyamide resin was 0.01 wt %.
  • a continuous fiber-reinforced resin composite material was obtained in the same manner as Example 1, except that during molding with the polyamide film, the polyamide resin and a carbon black master batch were dry blended and molded for use as a polyamide resin film.
  • the absorption percentage of the polyamide resin was 0.2 wt %.
  • the carbon black content was 90 ppm. In the Examples other than Example 6-4 and the Comparative Examples, no carbon black particulate additive was added.
  • a continuous fiber-reinforced resin composite material was obtained in the same manner as Example 6-1, except that the polyamide 66 used had an amount of carboxyl terminal groups of 50 ⁇ mol/g and an amount of carboxyl terminal groups of 30 ⁇ mol/g.
  • the absorption percentage of the polyamide resin was 0.2 wt %.
  • a continuous fiber-reinforced resin composite material was obtained in the same manner as Example 6-1, except that the polyamide 66 used had an amount of carboxyl terminal groups of 70 ⁇ mol/g and an amount of amino terminal groups of 50 ⁇ mol/g.
  • the absorption percentage of the polyamide resin was 0.2 wt %.
  • thermoplastic resin used was obtained by using a biaxial kneader to knead the polyamide 66 with 0.05 wt % sodium hypophosphite as a catalyst to promote reaction between the silane coupling agent and carboxyl terminal groups.
  • the absorption percentage of the polyamide resin was 0.2 wt %.
  • a continuous fiber-reinforced resin composite material was obtained in the same manner as Example 6-1, except that 0.05 wt % sodium hypophosphite was added to the sizing agent of the glass fibers.
  • the absorption percentage of the polyamide resin was 0.2 wt %.
  • a continuous fiber-reinforced resin composite material was obtained in the same manner as Example 6-2, except that a die open in the longitudinal direction was used as the die.
  • the absorption percentage of the polyamide resin was 0.2 wt %.
  • a continuous fiber-reinforced resin composite material was obtained in the same manner as Example 1, except that glass fibers without addition of a sizing agent were used.
  • a continuous fiber-reinforced resin composite material was obtained in the same manner as Example 6-1, except that the glass fibers used were adhered with a sizing agent that was 0.3 mass % of 3-glycidoxypropyltrimethoxysilane as a silane coupling agent, 1.5 mass % of an epoxy resin emulsion and 0.2 mass % of carnauba wax.
  • FIG. 4 shows a photograph of an interface region in the obtained molded article.
  • the continuous fiber-reinforced resin composite materials of Examples 6-1 to 6-9 exhibited very high tensile stress, flexural stress and flexural moduli due to reactivity of the coupling agent with the terminal functional groups in the thermoplastic resin.
  • thermoplastic resin When the flow rate of the thermoplastic resin was high during pressing as in Example 6-9, the coupling agent and the terminal functional groups in the thermoplastic resin failed to thoroughly react, and a reduction in physical properties was found.
  • Comparative Example 6-1 which used continuous reinforcing fibers not coated with a sizing agent
  • Comparative Example 6-2 which used continuous reinforcing fibers coated with a sizing agent containing a coupling agent with essentially no reactivity with the terminal groups of the resin, the tensile stress, flexural stress and flexural modulus were reduced.
  • a continuous fiber-reinforced resin composite material was obtained in the same manner as Example 7-1, except that glass fibers C were used as the continuous reinforcing fibers.
  • a continuous fiber-reinforced resin composite material was obtained in the same manner as Example 7-2, except that molding was carried out with a double belt apparatus.
  • Example 7-1 Evaluation was conducted in the same manner as Example 7-1, for “Tepex Dynalite 101” by Bond Laminate Co. comprising a glass cloth impregnated with polyamide 66.
  • Example 7-1 49.5 580 930 30 24.50 8.50
  • Example 7-2 53.2 590 940 30 25.50 8.70
  • Example 7-3 52.8 586 936 30 25.00 8.60 Comparative 29.3 380 560 23 16.08 5.32
  • Example 7-1 49.5 580 930 30 24.50 8.50
  • Example 7-2 53.2 590 940 30 25.50 8.70
  • Example 7-3 52.8 586 936 30 25.00 8.60
  • Example 7-1 49.5 580 930 30 24.50 8.50
  • Example 7-2 53.2 590 940 30 25.50 8.70
  • Example 7-3 52.8 586 936 30 25.00 8.60
  • Comparative 29.3 380 560 23 16.08 5.32
  • Example 7-1 49.5 580 930 30 24.50 8.50
  • Example 7-2 53.2 590 940 30 25.50 8.70
  • Example 7-3 52.8 586 936 30 25.00 8.60
  • Comparative 29.3 380 560
  • a continuous fiber-reinforced resin composite material was obtained in the same manner as Example 8-1, except that glass fibers C were used.
  • the ⁇ -drop formation coefficient between the glass fibers C and polyamide resin A was 27.
  • a continuous fiber-reinforced resin composite material was obtained in the same manner as Example 8-1, except that a film of polyamide resin C was used as the polyamide resin.
  • the ⁇ -drop formation coefficient between the glass fibers A and polyamide resin C was 3.
  • a continuous fiber-reinforced resin composite material was obtained in the same manner as Comparative Example 8-1, except that glass fibers C were used as the glass fibers.
  • the ⁇ -drop formation coefficient between the glass fibers C and polyamide resin C was 3.
  • a smartphone housing with the shape shown in FIG. 12 was fabricated.
  • One glass cloth using glass fibers C was sandwiched by polyamide resin A films and press molded.
  • the obtained molded article had a wall thickness of 0.4 mm, dimensions of 135 mm in the lengthwise direction and 65 mm in the widthwise direction, a lateral wall height of 5 mm, a tensile strength of 550 MPa and a flexural modulus of 35 MPa in the lengthwise direction, and a tensile strength of 530 MPa and a flexural modulus of 33 MPa in the widthwise direction.
  • As a result of measuring the electric field shield property at a flat section of the molded article by the KEC method it was found to have excellent electromagnetic wave transparency at 0 dB in the frequency band of 1 GHz.
  • the outer appearance of the molded article was satisfactory with no disorder of the fibers.
  • the tensile strength was measured according to JIS K7161.
  • the flexural modulus was measured according to JIS K7171.
  • the electric field shield property was measured by attaching a molded article cut out to a 5 cm ⁇ 5 cm square shape onto an aluminum sample-anchoring jig using conductive tape, applying electrolysis using an MA8602C electromagnetic wave shield property tester by Anritsu Co. (KEC method), and measuring the electrolytic shield characteristic at 1 GHz using an MS2661C spectrum analyzer by Anritsu Co.
  • HK-25D codirectional rotating twin-screw kneading extruder 41D
  • K-CL-24-KT20 weight-loaded twin-screw feeder by K-Tron Co. K-CL-24-KT20 weight-loaded twin-screw feeder by K-Tron Co.
  • the pellets were used to prepare a type A1, t4 mm molded multipurpose test piece conforming to JIS K 7139, using an electric injection molding machine (NEX140 by Nissei Plastic Industrial Co., Ltd., 140 tf mold clamping force/ ⁇ 40 screw diameter/full flight screw), under conditions according to JIS K 7152-1.
  • FIG. 10 shows an observational photograph of the interface taken during the preparation.
  • FIG. 11 shows an observational photograph of the interface taken during the preparation.
  • a satisfactory interface can be formed when the ⁇ -drop formation coefficient is 10 or greater and compatibility between the glass fibers and resin is satisfactory.
  • the continuous fiber-reinforced molded resin of the embodiment is industrially useful as a reinforcing material for materials that require a high level of mechanical properties, such as structural parts for various machines and vehicles, and also as a composite molded article material in thermoplastic resin compositions.
  • a continuous fiber-reinforced resin composite material of the invention it is possible to obtain a continuous fiber-reinforced resin composite material that has high adhesive force and affinity at the interfaces between the continuous reinforcing fibers and thermoplastic resin and low voids in the interfaces, and that exhibits sufficient strength.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Polymers & Plastics (AREA)
  • Manufacturing & Machinery (AREA)
  • Health & Medical Sciences (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Medicinal Chemistry (AREA)
  • Organic Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Composite Materials (AREA)
  • Inorganic Chemistry (AREA)
  • Textile Engineering (AREA)
  • Reinforced Plastic Materials (AREA)
  • Moulding By Coating Moulds (AREA)
  • Casting Or Compression Moulding Of Plastics Or The Like (AREA)
US16/970,904 2018-04-25 2019-04-23 Continuous-Fiber-Reinforced Resin Molding and Method for Manufacturing Same Abandoned US20200384704A1 (en)

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