JP7218517B2 - Fiber-reinforced plastic molding and method for producing the same - Google Patents

Description

TECHNICAL FIELD The present disclosure relates to fiber-reinforced plastic moldings and manufacturing methods thereof.

A sheet winding method is known as a method for manufacturing fiber-reinforced plastic moldings. In this sheet winding method, a prepreg sheet is wound. In this sheet winding method, a phenomenon (rising) occurs at the winding end edge of the sheet. Since the angle sheet does not have fibers along the longitudinal direction, it tends to rise up. Japanese Patent Application Laid-Open No. 2002-65194 discloses a prepreg tape wrapped around the outside of the angle sheet in order to prevent the angle sheet from "raising".

JP-A-2002-65194

When the angle sheets are wound to form the angle layers, seams of the sheets are inevitably formed. This seam exists along the entire axial direction. This seam can be the starting point of fracture. Also, the fibers are cut at the seams. This fiber break can be the starting point of fracture.

An object of the present disclosure is to provide a fiber-reinforced plastic molding having an angle layer with excellent strength.

In one aspect, the fiber-reinforced plastic molding has a longitudinal direction. This fiber-reinforced plastic molding may contain a fiber-reinforced plastic layer. The fiber-reinforced plastic layer may have an angle layer containing oblique fibers oriented obliquely with respect to the longitudinal direction. The angle layer may have a tape layer formed of a spirally extending tape-shaped prepreg. The tape-shaped prepreg may contain continuous fibers parallel to its extending direction. The continuous fibers may constitute the oblique fibers.

In another aspect, a method for manufacturing a fiber-reinforced plastic molded product includes a winding step of spirally winding a tape-shaped prepreg while applying tension to a base member including a mandrel, and after the winding step, and a mandrel removing step of removing the mandrel in a state in which the matrix resin contained in the tape-shaped prepreg is solidified. In the winding step, the tape-shaped prepreg may be wound while the tape width is adjusted by the tension.

In another aspect, a method for manufacturing a fiber-reinforced plastic molded product includes a winding step of spirally winding a tape-shaped prepreg while applying tension to a base member including a mandrel, and after the winding step, and a mandrel removing step of removing the mandrel in a state in which the matrix resin contained in the tape-shaped prepreg is solidified. In the winding step, the viscosity of the matrix resin may be such that the tape width can be changed by the tension.

A fiber-reinforced plastic molding having an angle layer with excellent strength can be provided.

FIG. 1 is a schematic diagram showing an example of a method for producing a fiber-reinforced plastic molding. 2(a) and 2(b) are diagrams for explaining the adjustment of the tape width. FIG. 3 is an exploded view showing the lamination structure of Examples 1 to 3. FIG. FIG. 4 is an exploded view showing the laminated structure of Comparative Example 1. FIG. FIG. 5 is a schematic diagram showing a method for measuring torsional fracture energy.

Hereinafter, the present disclosure will be described in detail based on preferred embodiments with appropriate reference to the drawings.

The fiber-reinforced plastic molding of the present disclosure has a longitudinal direction. For example, this fiber-reinforced plastic molding is a tubular body. The tubular body may have a varying outer diameter or a constant outer diameter. The tubular body may have a varying inner diameter or a constant inner diameter. If the centerline of the tubular body is straight, the direction of this centerline is the longitudinal direction.

Specific examples of this tubular body include golf club shafts, fishing rods, tennis racket frames, and drive shafts. It may be other than a tubular body.

FIG. 1 is a process drawing for explaining an example of a method for manufacturing the tubular body 200. FIG.

In the following description, the term “inner side” means the inner side of the tubular body in the radial direction, and the term “outer side” means the outer side of the tubular body in the radial direction. In the present application, "axial direction" means the axial direction of the tubular body.

The tubular body 200 is a laminate having one or more fiber reinforced resin layers. Tubular body 200 has a hollow structure.

A tape-shaped prepreg TP1 is used in manufacturing the tubular body 200 .

The tape-shaped prepreg TP1 is a tape containing fibers and matrix resin. The tape-shaped prepreg TP1 is cut out from a prepreg, for example. A typical tape-shaped prepreg TP1 is obtained by cutting a prepreg to a predetermined width.

In the tape-shaped prepreg TP1, fibers are oriented along its longitudinal direction. In the tape-shaped prepreg produced from the UD prepreg, the direction of the fibers aligned in one direction matches the longitudinal direction of the tape-shaped prepreg.

A tape-shaped prepreg TP1 can be produced simply by cutting a commercially available prepreg. As with prepregs, a variety of tape-shaped prepregs TP1 with different fiber types, thicknesses, fiber elastic moduli, fiber basis weights, prepreg basis weights, resin contents, etc. are commercially available. The tape-shaped prepreg TP1 has a specified thickness. Similar to prepreg, the tape-shaped prepreg TP1 has excellent thickness accuracy. The tape-shaped prepreg TP1 is excellent in thickness uniformity.

A prepreg is also called a prepreg sheet. A prepreg is a sheet-like material in which fibers are impregnated with resin. The impregnated resin is also called matrix resin. The matrix resin is preferably a thermosetting resin or a thermoplastic resin, more preferably a thermosetting resin.

The form of fibers in the prepreg is not limited. A typical prepreg is a UD prepreg. UD is an abbreviation for unidirection. In UD prepreg, the fibers are oriented substantially in one direction. As prepregs other than UD prepregs, for example, prepregs in which fibers are woven are known. A prepreg as a material of the tape-shaped prepreg TP1 is preferably a UD prepreg.

Many types of prepregs are commercially available. The type of fiber, thickness, fiber elastic modulus, fiber basis weight, prepreg basis weight, resin content, etc. differ depending on the type of prepreg. By using these prepregs, many kinds of tape-shaped prepregs TP1 can be produced.

Carbon fiber, glass fiber, aramid fiber, boron fiber, alumina fiber and silicon carbide fiber are exemplified as fibers used in the prepreg and tape-shaped prepreg TP1. Two or more of these fibers may be used in combination. Carbon fiber is preferable from the viewpoint of the strength of the molded article.

Examples of carbon fibers include PAN-based, pitch-based and rayon-based carbon fibers. From the viewpoint of tensile strength, PAN-based carbon fibers are preferred. The forms of carbon fibers include carbon fibers obtained by twisting and firing precursor fibers (so-called twisted yarn), carbon fibers obtained by untwisting the twisted yarn (so-called untwisted yarn), and precursor fibers that are substantially Examples include non-twisted yarns that are heat-treated without twisting. The carbon fibers may contain graphite fibers.

From the viewpoint of the strength and rigidity of the molded product, the tensile modulus of the fibers contained in the molded product is preferably 10 t/mm ² or more, more preferably 23.5 t/mm ² or more, preferably 70 t/mm ² or less, and 50 t. /mm ² or less is more preferable. This tensile modulus is measured according to JIS R 7601:1986 "Testing methods for carbon fiber".

From the viewpoint of the strength of the angle layer, the tensile modulus of the fibers contained in the tape-shaped prepreg TP1 is preferably 10 t/mm ² or more, more preferably 23.5 t/mm ² or more, preferably 70 t/mm ² or less, and 50 t/mm 2 or more. /mm ² or less is more preferable.

From the viewpoint of balance between weight reduction and strength, the fiber content in the molded product is preferably 65% by mass or more, more preferably 70% by mass or more, preferably 85% by mass or less, and more preferably 80% by mass or less. For the same reason, the fiber content in the tape-shaped prepreg TP1 is preferably 65% by mass or more, more preferably 70% by mass or more, preferably 85% by mass or less, and more preferably 80% by mass or less.

As the resin composition constituting the matrix resin of the tape-shaped prepreg TP1, an epoxy resin composition is preferable. The base resin of the epoxy resin composition is an epoxy resin. The epoxy resin component contained in this epoxy resin composition is preferably an epoxy resin having two epoxy groups in the molecule. In other words, the epoxy resin component preferably contains a bifunctional epoxy resin. Specific examples of bifunctional epoxy resins include bisphenol A type epoxy resin and its hydrogenated products, bisphenol F type epoxy resin and its hydrogenated products, bisphenol S type epoxy resin, tetrabromobisphenol A type epoxy resin, and bisphenol AD type epoxy resin. Bisphenol-type epoxy resins such as resins can be used. Bisphenol-type epoxy resins may be used alone or in combination of two or more. The epoxy resin composition preferably contains a curing agent. Typical curing agents include dicyandiamide. This curing agent can be combined with a curing aid for enhancing curing activity. As the curing aid, a urea derivative in which at least one of the hydrogens bonded to urea is substituted with a hydrocarbon group is preferred. The epoxy resin composition may further contain oligomers, polymer compounds, organic particles, inorganic particles, and the like.

An angle layer of the tubular body 200 is formed from the tape-shaped prepreg TP1.

A winding process is performed in manufacturing the tubular body 200 . As shown in FIG. 1, in this winding process, a tape-shaped prepreg TP1 is spirally wound around a base member 102 including a mandrel 100. As shown in FIG. By base member is meant the mandrel 100 or the mandrel 100 wrapped with other layers. Other layers wound around the base member are layers inside the angle layers formed by the tape-shaped prepreg TP1. In the embodiment of FIG. 1, base member 102 is mandrel 100 .

The tubular body 200 (fiber-reinforced plastic molding) may have angle layers other than the angle layers formed of the tape-shaped prepreg TP1. From the viewpoint of strength and weight reduction, it is preferable that the angle layers of the tubular body 200 (fiber-reinforced plastic molding) are only angle layers formed of the tape-shaped prepreg TP1.

In the winding process, tension F is applied to the wound tape-shaped prepreg TP1. The tape-shaped prepreg TP1 is wound while a tension F is applied. This winding process may be performed by an automatic machine or by human hands.

In this winding process, after the tape-shaped prepreg TP1 is wound, other layers are wound as necessary. Other layers constitute layers outside the tape-shaped prepreg TP1.

This winding step is preferably followed by a tape wrapping step and a heating step. Voids in the tubular body can be eliminated by tape wrapping. The heating step cures the thermosetting resin. Additionally, a mandrel stripping step is performed. In this mandrel removing step, the mandrel 100 is removed while the matrix resin contained in the tape-shaped prepreg is solidified. Further, if necessary, a tape wrapping removal step is performed. Furthermore, a surface polishing step may be performed. Thus, tubular body 200 is obtained.

The spirally wound tape-shaped prepreg TP1 forms one cylindrical layer as a whole. As described above, the fibers contained in the tape-shaped prepreg TP1 are arranged along the longitudinal direction of the tape-shaped prepreg TP1. Therefore, this fiber is arranged in a spiral like the tape-shaped prepreg TP1. The fibers are inclined with respect to the longitudinal direction (axial direction) of tubular body 200 .

A layer formed by this tape-shaped prepreg TP1 is an angle layer in the tubular body 200 . The angle (absolute value) of the fibers contained in the angle layer is preferably 20° or more, more preferably 30° or more, and still more preferably 40° or more with respect to the longitudinal direction (axial direction). The angle (absolute value) of the fibers contained in the angle layer is preferably 70° or less, more preferably 60° or less, and even more preferably 50° or less with respect to the longitudinal direction (axial direction).

2(a) and 2(b) show a method of adjusting the tape width W in the winding process.

In the winding process, the tape-shaped prepreg TP1 is wound while the tape width W is adjusted by the tension F. The tape width W is the width of the tape-shaped prepreg TP1.

In the winding process, the matrix resin of the tape-shaped prepreg TP1 is not solidified. Therefore, the tape width W of the tape-shaped prepreg TP1 is in a variable state. During the winding process, the tape width W can vary with the tension F. When the tension F increases, the fibers contained in the tape-shaped prepreg TP1 tend to gather together. Therefore, as the tension F increases, the tape width W decreases. The matrix resin of the tape-shaped prepreg TP1 is in a state where the tape width W can be changed by the tension F.

In this winding process, the tension F allows the tape width W to be adjusted. The greater the tension F, the smaller the tape width W. As FIG. 2(a) shows, a larger tape width W1 can be achieved when the tension F is a smaller tension F1. As FIG. 2(b) shows, a smaller tape width W2 can be achieved when the tension F is a greater tension F2. By increasing the tension F, the tape width W can be decreased. Also, by reducing the tension F, the tape width W can be increased.

The viscosity of the matrix resin is such that the tape width W can be adjusted by the tension F. If the viscosity is too high, the tape width W will not change even if the tension F is changed. From the viewpoint of adjustability of the tape width W, the viscosity of the matrix resin of the tape-shaped prepreg TP1 is preferably low. In the winding step, the viscosity of the matrix resin at the winding location M1 is preferably 1.0×10 ⁵ Pa·s or less, more preferably 1000 Pa·s or less, and even more preferably 100 Pa·s or less. If the viscosity is too low, the tackiness becomes excessive, and the handleability of the tape-shaped prepreg TP1 may deteriorate. On the other hand, if the viscosity is too low, the tape width W fluctuates too much, and the adjustment accuracy of the tape width W may deteriorate. From these points of view, the viscosity of the matrix resin at the winding portion M1 is preferably 5 Pa·s or more, more preferably 8 Pa·s or more, and even more preferably 10 Pa·s or more.

From the viewpoint of adjustability of the tape width W, it is preferable that the matrix resin of the tape-shaped prepreg TP1 is in the following state at the winding portion M1. When the matrix resin is a thermoplastic resin, the temperature of the resin is preferably higher than the glass transition temperature and lower than the decomposition initiation temperature (more preferably lower than the decomposition initiation temperature). If the matrix resin is a thermosetting resin, it is preferably in the B-stage. A B-stage resin is a thermosetting resin that is in an intermediate stage of the curing reaction. At the A stage, the handleability of the tape-shaped prepreg TP1 is deteriorated. At the C stage, the thermosetting resin is completely cured, so it is difficult to wind it around the base member. The A stage, B stage and C stage are defined in JIS K 6900-1994 (ISO 472:1988). From the viewpoint of ease of handling the tape-shaped prepreg TP1 during winding, the base resin of the matrix resin of the tape-shaped prepreg TP1 is preferably a thermosetting resin, more preferably an epoxy resin.

The winding location M1 is a position on the tape-shaped prepreg TP1 in the winding process, and means a boundary position between a portion in contact with the base member 102 and a portion not in contact with the base member 102 . In other words, the winding point M1 is the position where the winding starts. When the base member 102 is cylindrical, the winding location M1 is a linear portion along the axial direction.

From the viewpoint of adjustability of the tape width W, it is preferable to wind the tape-shaped prepreg TP1 while heating it in the winding step. This heating can achieve the preferred viscosities described above. In other words, it is preferred that the heating is done so as to achieve the desired viscosity. Heating is preferably done at the winding point M1. The areas to be heated are selected to allow adjustment of the tape width W.

A heater (heating device) is indicated by symbol HT in FIGS. 1, 2(a) and 2(b). Preferably, at least the winding point M1 is heated. Preferred heaters HT include infrared heaters.

In particular, this heating is preferably performed when the matrix resin is a thermosetting resin. This heating can achieve the preferred viscosity described above.

A tubular body 200 manufactured by such a method is an example of a fiber-reinforced plastic molding. This tubular body 200 has the following configuration.

The tubular body 200 includes a fiber-reinforced plastic layer, and this fiber-reinforced plastic layer has angle layers containing oblique fibers oriented obliquely with respect to the longitudinal direction of the tubular body 200 . This angle layer is a tape layer formed of a spirally extending tape-shaped prepreg TP1.

The tape-shaped prepreg TP1 contains continuous fibers parallel to its extending direction. This continuous fiber constitutes the oblique fiber. By inclining the tape-shaped prepreg TP1 with respect to the longitudinal direction of the tubular body 200, the fibers included in the tape-shaped prepreg TP1 are also inclined with respect to the longitudinal direction. The angle (absolute value) of the oblique fibers is preferably 20° or more, more preferably 30° or more, and still more preferably 40° or more with respect to the longitudinal direction (axial direction). The angle (absolute value) of the oblique fibers is preferably 70° or less, more preferably 60° or less, and even more preferably 50° or less with respect to the longitudinal direction (axial direction).

The tape-shaped prepreg TP1 contains a matrix resin and the continuous fibers. In forming the tape layer, the tape-shaped prepreg is wound while the tape width W is adjusted by tension F in a state in which the matrix resin is not solidified.

A cross-sectional view of the tape layer 110 is shown in the enlarged portion of FIG. 2(a). A cross-sectional view of the tape layer 120 is shown in the enlarged portion of FIG. 2(b). The tape layer 110 and the tape layer 120 are formed from the same tape-shaped prepreg TP1. Nevertheless, tape layers 110 and 120 are different. In tape layer 110 , tape edge 112 overlaps adjacent tape edge 114 . That is, tape layer 110 has an overlap. On the other hand, in tape layer 120 , tape edge 112 does not overlap adjacent tape edge 114 . That is, in the tape layer 120, the tape-shaped prepreg TP1 is spirally wound without overlapping.

Further, in tape layer 120 , tape edge 112 abuts adjacent tape edge 114 . That is, in the tape layer 120, the tape-shaped prepreg TP1 is spirally wound with substantially no gaps. In the present application, the term “substantially no gap” means that the gap is 0.2 mm or less, more preferably 0.1 mm or less, and still more preferably 0.05 mm or less. can be omitted.

In the tape layer 110 shown in FIG. 2(a), a space R1 is formed due to the presence of the overlap. In the heating process, resin flows into this space R1 to form a resin pool. This resin pool is weak because it does not contain carbon fiber. A resin puddle can be a starting point of destruction. A resin puddle reduces the strength of the molding.

In the tape layer 120 shown in FIG. 2(b), resin pools are not formed due to the absence of the overlap. For this reason, the strength of the molding is increased.

It is difficult to wind the tape-shaped prepreg TP1 without gaps. Even if the winding angle is adjusted according to the tape width W, if the winding angle is slightly deviated, an overlap occurs. Moreover, when the mandrel 100 has a taper, the winding angle inevitably changes, so it is difficult to wind the tape-shaped prepreg TP1 without gaps.

In the above embodiment, since the tape width W can be adjusted by the tension F, the tape-shaped prepreg TP1 can be wound substantially without gaps. Therefore, the formation of resin pools is suppressed, and a strong angle layer can be formed. In addition, the angle plies do not have sheet seams, such as those found in sheet winding processes. Furthermore, in this angle layer, the fibers are continuous without being broken. Therefore, this angle layer is excellent in strength. This angle layer enhances the strength of the molding, particularly torsional strength.

This embodiment has the following effects as compared with the filament winding method.

A tow prepreg is used in the filament winding method. This tow prepreg has a cross-sectional shape closer to a circle and a lower cross-sectional accuracy than the tape-shaped prepreg TP1. Therefore, it is difficult to adjust the gap with high accuracy. In addition, resin pools are likely to be formed due to the nearly circular cross-sectional shape.

Moreover, at room temperature, the tow prepreg has a low resin viscosity and is sticky. Therefore, the tow prepreg is inferior to the tape-shaped prepreg TP1 in handleability and workability. The tape-shaped prepreg TP1 is excellent in handleability and workability. Preferably, the viscosity of the matrix resin of the tape-shaped prepreg TP1 is 10000 Pa·s or more and 200000 Pa·s or less at 20°C.

In the tape-shaped prepreg TP1, the viscosity can be locally reduced only at the heated portions, and the high viscosity can be maintained at the unheated portions. Therefore, it is possible to achieve both adjustability of the tape width W and ease of handling.

Although the effects of the present disclosure will be clarified by examples below, the present disclosure should not be construed in a limited manner based on the description of the examples.

[Example 1]
FIG. 3 is an exploded view showing the laminated structure of the tubular body of Example 1. FIG. In this Example 1, eight prepreg sheets from the first sheet S1 to the eighth sheet S8 were used. The first sheet S1 and the second sheet S2 were tape-shaped prepreg TP1. The third sheet S3 to the eighth sheet S8 were square prepreg sheets used in a normal sheet winding method. Fibers are cut on all four sides of this square.

The following prepregs were used for each sheet. The sheets S1 and S2 were obtained by cutting the following prepreg into tapes along the carbon fibers.
・ First sheet S1: 805S-3 (manufactured by Toray Industries, Inc.)
・Second sheet S2: 805S-3 (manufactured by Toray Industries, Inc.)
・Third seat S3: TR350C-150S (manufactured by Mitsubishi Rayon)
・Fourth seat S4: TR350C-100S (manufactured by Mitsubishi Rayon Co., Ltd.)
・ Fifth sheet S5: 805S-3 (manufactured by Toray Industries, Inc.)
・Sixth seat S6: TR350C-100S (manufactured by Mitsubishi Rayon)
・Seventh sheet S7: 805S-3 (manufactured by Toray Industries, Inc.)
・8th seat S8: TR350C-100S (manufactured by Mitsubishi Rayon Co., Ltd.)

The first sheet S1 and the second sheet S2 are angle layers. The fibers of the sheet S1 and the fibers of the sheet S2 are inclined in opposite directions. The third sheet S3 is a straight layer. In the straight layer, the fibers are oriented along the axial direction and the fiber angle is 0° with respect to the axial direction. The fourth sheet S4 is also a straight layer. The fifth sheet S5 is a hoop layer. In the hoop layer, the fibers are perpendicular to the axial direction and the fiber angle is 90° to the axial direction. The sixth sheet S6 is a straight layer. The seventh sheet S7 is a hoop layer. The eighth sheet S8 is a straight layer.

A mandrel 100 with a constant outer diameter was prepared. The mandrel 100 was set on a jig, and the sheet S1 (tape-shaped prepreg) was helically wound around the mandrel 100 while rotating the mandrel 100 . Winding was performed while adjusting the tension F by hand. As shown in FIG. 1, the sheet S1 was wound while heating the winding location M1 with the heater HT. As the heater HT, a short wavelength infrared heater "ZKB600/80G" manufactured by Helius was used. The extending direction of the sheet S1 (tape) was +45° with respect to the axial direction of the mandrel 100 . Therefore, the fibers CF included in the sheet S1 were also oriented at +45° with respect to the axial direction of the mandrel 100. Next, a sheet S2 (tape-shaped prepreg) was spirally wound in the same manner as the sheet S1. The extending direction of the sheet S2 (tape) was −45° with respect to the axial direction of the mandrel 100. FIG. Therefore, the fibers CF contained in the sheet S2 were also oriented at −45° with respect to the axial direction of the mandrel 100. FIG. Subsequently, sheets S3 to S8 were sequentially wound by a normal sheet winding method.

After the winding process was finished, the wrapping tape was wrapped and heated in an oven at a temperature of 130° for 2 hours. After that, the mandrel was pulled out, the wrapping tape was removed, and the tubular body of Example 1 was obtained. The length of the tubular body was 400 mm.

In the winding process of Example 1, the viscosity of the matrix resin of the sheet S1 and the sheet S2 at the winding location M1 was 10 Pa·s.

[Example 2]
A tubular body of Example 2 was obtained in the same manner as in Example 1, except that the degree of heating by the heater HT was adjusted so that the viscosity of the matrix resin of the sheets S1 and S2 at the winding portion M1 was 5 Pa·s. rice field.

[Example 3]
A tubular body of Example 3 was obtained in the same manner as in Example 1, except that the degree of heating by the heater HT was adjusted so that the viscosity of the matrix resin of the sheets S1 and S2 at the winding portion M1 was 100000 Pa·s. rice field.

[Comparative Example 1]
FIG. 4 is a developed view showing the laminated structure of the tubular body of Comparative Example 1. FIG. Also in Comparative Example 1, eight prepreg sheets from the first sheet S1 to the eighth sheet S8 were used. The product number of each sheet was the same as in Examples 1-3. The weight of each sheet was also the same as in Examples 1-3. However, the first sheet S1 and the second sheet S2 were not tape-shaped. That is, the first sheet S1 and the second sheet S2 were square prepreg sheets used in a normal sheet winding method. Fibers are cut on all four sides of this square sheet. As in Examples 1 to 3, the fiber orientation was +45° for sheet S1 and -45° for sheet S2. Otherwise, the tubular body of Comparative Example 1 was obtained in the same manner as in Example 1.

[Evaluation method]
The torsional fracture energy of the obtained tubular body was evaluated by the following method.

[Torsion breaking energy]
FIG. 5 shows a method for measuring torsional fracture energy. As a tester, a golf shaft torsion fracture tester "TT9501" manufactured by Fawick Japan Co., Ltd. was used. One end of tubular body 200 was fixed to jig G1 over a length of 50 mm. The other end of tubular body 200 was fixed to jig G2 over a length of 50 mm. The distance (span) between the jig G1 and the jig G2 was set to 300 mm. The jig G2 was rotated with respect to the jig G1 at a rotation speed of 110 (deg/sec), and the deformation angle θ (degree) and the torque T (N·m) when torsional failure occurred were measured. Torsional breaking energy (Nm·deg) is calculated by θ×T.

The torsional fracture energies of Examples 1 to 3 and Comparative Example 1 were as follows. These values are shown as ratios to Comparative Example 1.
・Example 1: 1.31
・Example 2: 1.17
- Example 3: 1.08
・Comparative Example 1: 1.00

In Examples 1 to 3, in the process of winding the sheets S1 and S2, the tension F was adjusted to eliminate overlap and minimize the gap between the tape edges. However, since there was a difference in adjustability of the tape width W depending on the viscosity of the matrix resin, there was a difference in torsional breaking energy between Examples 1 to 3. On the other hand, in Comparative Example 1, the angle sheets S1 and S2 had seams, and the fibers were cut at the seams.

From the above evaluation results, the superiority of the present disclosure is clear.

The following remarks are disclosed with respect to the above-described embodiments.
[Appendix 1]
A fiber-reinforced plastic molding having a longitudinal direction,
contains a fiber-reinforced plastic layer,
The fiber-reinforced plastic layer has an angle layer containing oblique fibers oriented obliquely with respect to the longitudinal direction,
The angle layer has a tape layer formed of a spirally extending tape-shaped prepreg,
A fiber-reinforced plastic molded product, wherein the tape-like prepreg contains continuous fibers parallel to its extending direction, and the continuous fibers constitute the oblique fibers.
[Appendix 2]
The tape-shaped prepreg contains a matrix resin and the continuous fibers,
The fiber-reinforced plastic molded product according to appendix 1, wherein in the formation of the tape layer, the tape-shaped prepreg is wound while the tape width is adjusted by tension while the matrix resin is not solidified.
[Appendix 3]
The fiber-reinforced plastic molded article according to appendix 2, wherein in the tape layer, the tape-shaped prepreg is spirally wound without overlapping.
[Appendix 4]
3. The fiber-reinforced plastic molding according to appendix 3, wherein in the tape layer, the tape-shaped prepreg is spirally wound with substantially no gaps.
[Appendix 5]
5. The fiber-reinforced plastic molding according to any one of Appendices 1 to 4, wherein the base resin of the matrix resin is an epoxy resin.
[Appendix 6]
6. The fiber-reinforced plastic molding according to any one of Appendices 1 to 5, wherein the fibers contained in the fiber-reinforced plastic layer are carbon fibers.
[Appendix 7]
7. The fiber-reinforced plastic molding according to any one of appendices 1 to 6, which is a golf club shaft.
[Appendix 8]
A winding step of spirally winding a tape-shaped prepreg while applying tension to a base member including a mandrel;
a mandrel removing step of removing the mandrel after the winding step and removing the mandrel in a state in which the matrix resin contained in the tape-shaped prepreg is solidified;
The method for producing a fiber-reinforced plastic molding, wherein the winding step includes winding the tape-shaped prepreg while adjusting the tape width by the tension.
[Appendix 9]
The manufacturing method according to appendix 8, wherein in the winding step, the viscosity of the matrix resin at the winding location is 5 Pa·s or more and 1.0×10 ⁵ Pa·s or less.
[Appendix 10]
10. The manufacturing method according to appendix 8 or 9, wherein in the winding step, the tape-shaped prepreg is wound while being heated.
[Appendix 11]
A winding step of spirally winding a tape-shaped prepreg while applying tension to a base member including a mandrel;
a mandrel removing step of removing the mandrel after the winding step and removing the mandrel in a state in which the matrix resin contained in the tape-shaped prepreg is solidified;
In the winding step, the viscosity of the matrix resin is such a viscosity that the tape width can be changed by the tension.

The present disclosure can be applied to any fiber-reinforced plastic molding including tubular bodies.

DESCRIPTION OF SYMBOLS 100... Mandrel 102... Base member 200... Tubular body (fiber reinforced plastic molding)
TP1: Tape-shaped prepreg HT: Heater W: Tape width S1 to S8: Prepreg sheet

Claims (4)

A winding step of spirally winding a tape-shaped prepreg while applying tension to a base member including a mandrel;
a mandrel removing step of removing the mandrel after the winding step and removing the mandrel in a state in which the matrix resin contained in the tape-shaped prepreg is solidified;
The tape-shaped prepreg is made of a UD prepreg sheet molded into a sheet with a specified thickness and resin content,
In the winding step, the tape-shaped prepreg is heated and wound while the tape width is adjusted by the tension while the matrix resin is not solidified. In the winding step, the tape-shaped prepreg is wound while being heated while adjusting the tape width by the tension so that the tape-shaped prepreg is spirally wound with no overlap and substantially no gap. The manufacturing method according to claim 1 . 3. The manufacturing method according to claim 2 , wherein in the winding step, the viscosity of the matrix resin at the winding location is 5 Pa.s or more and ^{1.0.times.10.sup.5} Pa.s or less. 4. The manufacturing method according to any one of claims 1 to 3 , wherein in the winding step, the viscosity of the matrix resin is such that the tape width can be changed by the tension.

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