JP5504859B2 - Carbon fiber precursor fiber bundle, carbon fiber bundle and their production method - Google Patents

Description

  The present invention relates to a modified cross-section carbon fiber bundle that is made of single fibers having different cross-sectional shapes and gives a prepreg having a high fiber content.

  Since carbon fiber has higher specific strength and specific modulus than other fibers, it can be used as a reinforcing fiber for composite materials in addition to conventional sports applications, aerospace applications, automobiles, civil engineering / architecture, pressure vessels and It is being widely deployed in general industrial applications such as windmill blades, and there is a strong demand for higher performance.

  Among the carbon fibers, the most widely used polyacrylonitrile-based carbon fiber is a polyacrylonitrile-based fiber bundle that becomes a polyacrylonitrile-based precursor, obtained by wet spinning or dry-wet spinning, and then heated at 200 to 400 ° C. It is industrially produced by converting to a flame-resistant fiber bundle in an oxidizing atmosphere, carbonizing in an inert atmosphere of at least 1000 ° C., and graphitizing at about 2000 ° C. or higher if necessary.

  In the case of producing a composite material using carbon fibers, it is desirable that a thin composite material having desired strength and elastic modulus is obtained from the viewpoint of performance and cost. As a method of obtaining the same strength characteristics as in the conventional case when the composite material is thinned, there is a method of increasing the carbon fiber content (Vf). In this case, it is effective to reduce the dead space between the fibers, but as the technique, a technique using a fiber having a flat cross-sectional shape (see Patent Document 1), a different fiber diameter or a different cross-sectional area is used. There has been proposed a method for producing a non-woven fabric from fibers it has (see Patent Documents 2 and 3). However, both relate to a method for producing a paper-like material or a nonwoven fabric, and since fibers are not aligned in one direction, it is essentially difficult to increase Vf. Further, in producing a carbon fiber bundle composed of single fibers having different fiber diameters, it can be obtained by combining a plurality of carbon fiber bundles having different finenesses. The fibers must be dispersed and arranged efficiently, and the fibers can be entangled by applying excessive force to the fibers, resulting in damage to the carbon fibers and reduced strength characteristics. There is a problem that it is difficult to increase Vf.

  In addition, polyacrylonitrile fiber bundles with different fineness can be obtained from a die having a different diameter of the die diameter from the beginning, but there is no example for carbon fiber, and the fineness is large because it is for clothing characterized by texture. (See Patent Documents 4 to 6). In addition to simply increasing the fineness, if the fineness is reduced, there is a drawback that spinning cannot be stably performed because of a large difference in the spinning draft.

  On the other hand, in order to produce carbon fibers excellent in adhesiveness to resin, bending strength and compressive strength, methods have been proposed for obtaining deformed cross-section fibers having a second moment of section higher than circular (Patent Documents 7 and 8). However, there is a problem that it is difficult to increase Vf.

Japanese Patent Laid-Open No. 2004-027435 Japanese Patent Laid-Open No. 11-172559 JP-A-2-234918 Japanese Patent Publication No. 60-2405 Japanese Examined Patent Publication No.59-47725 JP-A-11-217740 JP-A-11-302916 Japanese Patent No. 2550807

  An object of the present invention is to provide a modified cross-section carbon fiber bundle that is excellent in adhesiveness with a resin, bending strength, and compressive strength, and that can obtain a prepreg composed of single fibers having different cross-sectional shapes.

The present invention has the following configuration. That is,
( I ) In the fiber diameter distribution, the number average fiber diameter in the range from the fiber diameter 25% smaller than the maximum fiber diameter to the maximum fiber diameter is R1, and the number average fiber diameter of the other single fibers is R2. The fiber diameter ratio R defined by the following formula (1) is 0.2 to 0.7, R1 is 4 to 7 μm, the number N2 corresponding to R2, and the number N1 corresponding to R1. Sometimes the mixing ratio defined by N = N2 / N1 is 0.5-2, the strand tensile elongation of the carbon fiber bundle is 1.0-3.0%, and the number average of the cross section of the single fiber A carbon fiber bundle having a roundness of 0.1 to 0.85 and a basis weight of 0.1 g / m or more.

R = R2 / R1 Formula (1)
(Ii) in the distribution of fiber diameter, the number average fiber diameter in the range up to the maximum fiber diameter 25% smaller fiber diameter relative to the largest fiber diameter and R '1, the number-average fiber diameter of other monofilament When R ′ 2, the fiber diameter ratio R ′ defined by the following formula (3) is 0.2 to 0.7, R ′ 1 is 6 to 11 μm, and the number N corresponding to R′2 When the number N′1 corresponding to “2, R′1” is set, the blend ratio defined by N ′ = N′2 / N′1 is 0.5 to 2, and the raw crystal orientation degree is 86 A polyacrylonitrile-based carbon fiber precursor fiber bundle having a weight of ˜91% and a basis weight of 0.2 g / m or more. (Hereinafter, polyacrylonitrile may be abbreviated as PAN . )
R ′ = R′2 / R′1 Formula (3)
(Iii) polyacrylonitrile-based polymer solution was dry-wet spinning, a method for obtaining a carbon fiber precursor fiber bundle to a draw ratio after solidification take-up to 7 to 15 times, 0.3 the spinneret hole pitch 0.9 mm , the number of holes in the die is set to 6000 to 30000, the air gap distance between the spinneret and the coagulation bath liquid surface is set to 1 to 5 mm, and the basis weight of the carbon fiber precursor fiber bundle is 0.2 g / A method for producing a carbon fiber precursor fiber bundle, wherein spinning is performed by adjusting a discharge amount of the polyacrylonitrile-based polymer solution so as to be m or more .
( Iv ) The polyacrylonitrile-based carbon fiber precursor fiber bundle described in (ii) above or the carbon fiber precursor fiber obtained by the production method described in ( iii ) above is air at a temperature of 200 to 300 ° C. Flame-proofing step for making flame resistant inside, pre-carbonizing step for pre-carbonizing the fiber obtained in the flame-proofing step in an inert atmosphere at a temperature of 300 to 800 ° C., and 1 for the fiber obtained in the pre-carbonizing step , Ru successively passed through a carbonization step of carbonizing in an inert atmosphere at a temperature of 000～3,000 ° C., method of producing a carbon fiber bundle.

  According to the present invention, it is possible to obtain a carbon fiber bundle for a composite material that achieves excellent static tensile, compression, and impact properties while achieving weight reduction of the member by thinning the composite material.

  The carbon fiber bundle of the present invention has a weight per meter (hereinafter also referred to as basis weight) of 0.1 g / m or more. Since the carbon fiber weight is large as described above, the amount that can be produced at one time by a limited-sized production apparatus is increased, and the productivity at the time of production is greatly improved, so that production at low cost is possible. From such a viewpoint, the basis weight of the carbon fiber bundle is more preferably 0.2 g / m or more, and 10 g / m is sufficient. As will be described later, in order to obtain the cross-sectional shape of the single fiber of the present invention, the single fiber may be fused and spun, so that the number of holes in the die and the number of single fibers in the carbon fiber bundle may not match. Yes, the amount of the carbon fiber bundle of the present invention can be adjusted by the basis weight at the time of spinning the precursor fiber bundle.

The single fiber constituting the carbon fiber bundle of the present invention has the following specific fiber diameter distribution and cross-sectional shape. The specific fiber diameter distribution is obtained by spinning a carbon fiber precursor fiber obtained by spinning with a spinneret having 1 to 3 kinds of pore diameters, and fusing a spinning solution for 1 to 6 holes before solidification. Can be obtained.
In addition, in this invention, a fiber diameter is an equivalent area circle equivalent diameter of the cross section of each single fiber. As a method for obtaining an image for measuring the fiber diameter distribution of carbon fibers for obtaining such a fiber diameter, there is a direct observation using an optical microscope or a laser microscope, or a method using a scanning electron microscope (SEM). When observing the fiber bundle at once, a method of cutting the carbon fiber bundle with a sharp blade and observing the cross section with an optical microscope or a laser microscope is suitable. An image obtained by these methods is subjected to image analysis, a cross-sectional area is obtained, and a fiber diameter can be obtained by converting it into a diameter when it is assumed to be a circle. And the data of this fiber diameter are suitably collected in the range of 500-1500, and distribution of a fiber diameter is calculated | required.
In the present invention, the fiber diameter distribution of the single fibers constituting the carbon fiber bundle needs to satisfy the following three conditions.
As a first condition, the number average fiber diameter in the range from the maximum fiber diameter in the carbon fiber bundle to the fiber diameter 25% smaller than the maximum fiber diameter is R1, and the number average fiber diameter of other single fibers Is R2, the fiber diameter ratio R defined by the following formula (1) needs to be 0.2 to 0.7. The range of R is preferably 0.2 to 0.6, and more preferably 0.3 to 0.5.

R = R2 / R1 Formula (1)
In the conventional carbon fiber, the single fiber constituting the carbon fiber bundle has a fiber diameter distribution having one maximum value, and generally the carbon fiber bundle has higher composite material properties as the distribution of the single fiber diameter is narrower. Commercially available carbon fiber bundles often contained all single fibers in the range from the fiber diameter 15% smaller than the maximum fiber diameter to the maximum fiber diameter in the distribution of the fiber diameter of the single fibers. In such a carbon fiber, there is a theoretical limit to the close-packed Vf, and it is extremely difficult to bring the fiber bundle arrangement into the close-packed state. In the present invention, by setting R in the above range and the single fiber having a specific cross-sectional shape, the fundamental limit of Vf is increased, and it becomes easy to increase Vf.

  As a second condition, the carbon fiber bundle of the present invention needs to have R1 of 4 to 7 μm. This is because it is important that the carbon fiber has such a fiber diameter in order to exhibit high strength, and is preferably 4 to 6 μm. When R1 exceeds 7 μm, the physical property balance of the composite material as a whole is poor, and when R1 is 3 μm or less, R2 becomes too small and processability is deteriorated.

  As a third condition, in the present invention, when the number N2 corresponding to R2 and the number N1 corresponding to R1, the blend ratio defined by N = N2 / N1 needs to be 0.5-2. Preferably, it is 0.8-1.2, More preferably, it is 0.9-1.1. This is because, in the range of the diameter ratio R defined in the present invention, the blending ratio N is closer to 1, and Vf is easily increased. When N exceeds 2, it is difficult to increase Vf unless R is reduced. When N is less than 0.5, the effect of increasing Vf is insufficient.

  Moreover, in order to express the effect which improves a fiber content rate effectively, it is preferable that a thin fiber is adjacent to a thick fiber in a carbon fiber bundle.

  The strand tensile elongation required for the carbon fiber bundle of the present invention is 1.0 to 3.0%, preferably 1.2 to 3.0%. This is because if the strand tensile elongation is low, the tensile strength of the composite material cannot be increased. The higher the strand tensile elongation, the better. However, in reality, the upper limit is about 3%, so this was set as the upper limit. It should be noted that if a carbon fiber having a higher elongation is obtained in the future, this does not prevent the application.

  The carbon fiber bundle of the present invention is formed by bundling 3000 or more single carbon fibers. Since the number of single fibers is large in this way, the amount that can be produced at one time by a limited-sized production apparatus is increased, and the productivity at the time of production is greatly improved, so that production at low cost becomes possible. From this viewpoint, the number of single fibers constituting the carbon fiber bundle is preferably 12,000 or more, more preferably 24000 or more. On the other hand, if the total fineness of the carbon fiber bundle becomes too high, the carbon fiber bundle becomes short due to the limit of the package diameter that can be wound per carbon fiber package, and the product using the carbon fiber bundle (intermediate) The number of single fibers constituting the carbon fiber bundle is preferably 100,000 or less. The number of single fibers is obtained by dividing the cross sectional area of the carbon fiber bundle by the average single fiber cross sectional area.

  In the present invention, Vf can be increased by appropriately arranging single fibers having a specific fiber diameter distribution and different cross-sectional shapes. That is, the number average roundness of the cross section of the single fiber constituting the carbon fiber bundle of the present invention is 0.1 to 0.85, and preferably 0.45 to 0.75. In the present invention, the roundness refers to the SEM observation of the cross section of the carbon fiber bundle in the same manner as the previous fiber diameter, and the image is analyzed to determine the cross-sectional area S of the single fiber and the peripheral length L of the single fiber, It is a value obtained by using the following formula (2), and the number average roundness is defined as the number average roundness.

Roundness = 4πS / L ² (2)
By making the cross-sectional shape non-circular with a roundness of 0.1 to 0.85 as in the present invention, the buckling of the carbon fiber can be suppressed and the properties such as the compressive strength of the composite material can be enhanced. .

  In a preferred embodiment of the present invention, the variation coefficient of the roundness of the cross section of the single fiber constituting the carbon fiber bundle is 20 to 80%. When the roundness has a wide distribution, characteristics such as compressive strength can be improved when the Vf of the composite material is increased.

  In addition, as shown in JP-A-11-124743, etc., the bending rigidity of the carbon fiber is improved by deforming the cross-sectional shape of the single fiber from a perfect circle (hereinafter sometimes referred to as “deformed”). In a carbon fiber bundle composed of single fibers having a relatively simple irregular cross section such as flat or three leaves, the single fibers are engaged with each other, and the spreadability is reduced. . On the other hand, for carbon fiber bundles composed of single fibers having complex irregular cross sections such as 8-leaf or C-shaped, the single fibers are unlikely to mesh with each other, but conversely, the single fibers are closely packed as carbon fiber bundles. When the prepreg is manufactured, the carbon fiber content cannot be increased, and the mechanical properties of the composite material are deteriorated.

  Next, the manufacturing method of the precursor fiber bundle suitable for obtaining the carbon fiber bundle of this invention is demonstrated.

  A technique for producing a carbon fiber precursor fiber that gives excellent spinnability by using a PAN-based polymer having a specific molecular weight distribution has already been proposed (Japanese Patent Laid-Open No. 2008-248219). During the study, it was found that precursor fiber bundles having similar fiber structures and different fineness and cross-sectional shapes can be easily obtained, and the present invention has been achieved. In order to obtain precursor fibers with different fineness and different cross-sectional shapes, it is necessary to obtain a precursor fiber by discharging a spinning solution and fusing it before coagulation. is important. In the dry-wet spinning method, generally, the relationship between the initial tension of the spinning solution immediately after discharge and the tension and weight of the spinning solution before coagulation is important. If they are fused together, the spinnability is greatly reduced. However, in the spinning solution used in the present invention, the spinning draft is easily increased by the spinning draft, so that the spinnability is enhanced.

  The spinning solution suitably used in the present invention is obtained by dissolving a PAN-based polymer in which Mz / Mw, which is a ratio of the Z average molecular weight Mz and the weight average molecular weight Mw, is 2.7 or more, in a solvent. Since the PAN-based polymer having such a molecular weight distribution contains a polymer component having a large molecular weight, the effects of the present invention are remarkably exhibited.

  First, the PAN polymer that can be suitably used in the present invention will be described. In the present invention, the Z average molecular weight (hereinafter abbreviated as Mz) measured by a gel permeation chromatograph (hereinafter abbreviated as GPC) method (the details of the measurement method will be described later) is 800,000 to 600. The polydispersity (Mz / Mw) (Mw represents a weight average molecular weight, hereinafter abbreviated as Mw) is 2.7-10. Mz is preferably 2 million to 6 million, more preferably 2.5 million to 4 million, and further preferably 2.5 million to 3.2 million. Moreover, polydispersity (Mz / Mw) becomes like this. Preferably it is 5-8, More preferably, it is 5.5-7.

  The index regarding the average molecular weight and molecular weight distribution measured by the GPC method will be described below.

The average molecular weight measured by the GPC method includes a number average molecular weight (hereinafter abbreviated as Mn), a weight average molecular weight (Mw), a z average molecular weight (Mz), and a Z + 1 average molecular weight (M _{Z + 1} ). Mn is sensitively influenced by the low molecular weight substances contained in the polymer compound. On the other hand, Mw receives the contribution of a high molecular weight substance more sensitively than Mn. Mz is more sensitive to the contribution of high molecular weight than Mw, and the Z + 1 average molecular weight (hereinafter abbreviated as M _{Z + 1} ) is more sensitive to the contribution of high molecular weight than Mz.

The molecular weight distribution obtained using the average molecular weight measured by the GPC method includes molecular weight distribution (Mw / Mn) and polydispersity (Mz / Mw and M _{Z + 1} / Mw). The status of molecular weight distribution can be shown. When the molecular weight distribution (Mw / Mn) is 1, it is monodisperse, whereas as the molecular weight distribution (Mw / Mn) becomes larger than 1, the molecular weight distribution becomes broader around the low molecular weight side. As the polydispersity (Mz / Mw) becomes larger than 1, the molecular weight distribution becomes broader around the high molecular weight side. Also, as the polydispersity (M _{Z + 1} / Mw) becomes larger than 1, the molecular weight distribution becomes broader around the high molecular weight side. In particular, the polydispersity (M _{Z + 1} / Mw) is significantly increased when two types of polymers having significantly different Mw are mixed. Here, the molecular weight measured by GPC method shows the molecular weight of polystyrene conversion. The larger the polydispersity (Mz / Mw), the better. If Mz is in the range of 800,000 to 6 million, sufficient strain hardening occurs when the polydispersity (Mz / Mw) is 2.7 or more. The degree of improvement in ejection stability of the spinning solution containing coalescence is sufficient. In addition, when the polydispersity (Mz / Mw) is too large, strain hardening is too strong, and the effect of improving the discharge stability of the spinning solution containing the PAN-based polymer may be reduced. When the polydispersity (Mz / Mw) is 10 or less within the range of 6 million, the degree of improvement in ejection stability of the spinning solution containing the PAN-based polymer is sufficient. In addition, when the polydispersity (Mz / Mw) is in the range of 2.7 to 10, if the Mz is less than 800,000, the strength of the precursor fiber may be insufficient, and if the Mz is greater than 6 million, the discharge is difficult. There is a case.

  In addition, Mw / Mn is preferably as small as possible because the smaller the content of low molecular components that are likely to be structural defects of the carbon fiber, and Mw / Mn is preferably smaller than Mz / Mw. That is, even if it is broad on both the high molecular weight side and the low molecular weight side, there is little decrease in ejection stability, but the low molecular weight side is preferably as sharp as possible, and Mz / Mw is higher than Mw / Mn. It is preferably 1.5 times or more, and more preferably 1.8 times or more. According to the study by the present inventors, in radical polymerization such as aqueous suspension or solution method, which is usually performed in the polymerization of acrylonitrile (hereinafter abbreviated as AN), the molecular weight distribution has a lower molecular weight side. Therefore, Mw / Mn becomes larger than Mz / Mw. Therefore, when performing polymerization under special conditions such as the type and ratio of the polymerization initiator and sequential addition, or when using general radical polymerization, there is a method of mixing two or more PAN-based polymers. The method of mixing is simple. The smaller the number of types to be mixed, the easier and the two types are often sufficient from the viewpoint of ejection stability.

  The Mw of the polymer to be mixed is a PAN-based polymer having a large Mw as the A component, and a PAN-based polymer having a small Mw is the B component. Is 1 million to 5 million, and Mw of the B component is preferably 50,000 to 900,000. The larger the difference between the Mw of the A component and the B component, the greater the Mz / Mw of the mixed polymer tends to increase. This is a preferred embodiment, but when the Mw of the A component is greater than 15 million, production of the A component When the Mw of the B component is less than 150,000, the strength of the precursor fiber may be insufficient, and it is realistic that Mz / Mw is 10 or less.

  Specifically, the ratio of the weight average molecular weight of the A component and the B component is preferably 4 to 45, and more preferably 20 to 45.

  The weight ratio of the A component and the B component is preferably 0.003 to 0.3, more preferably 0.005 to 0.2, and 0.01 to 0.1. Further preferred. When the weight ratio of the A component to the B component is less than 0.003, strain hardening may be insufficient, and when it is greater than 0.3, the discharge viscosity of the polymer solution may increase so that the discharge may become difficult.

  When mixing the polymer of component A and component B, a method of mixing both polymers and then diluting with a solvent, a method of mixing each of the polymers diluted in a solvent, and a high molecular weight material that is difficult to dissolve A method in which the B component is mixed and dissolved after diluting the A component in the solvent, and a solution in which the monomer constituting the B component is mixed with a solution obtained by diluting the high molecular weight A component in the solvent. It is possible to employ a mixing method. For mixing, a method of stirring in a mixing tank, a method of quantifying with a gear pump or the like and mixing with a static mixer, a method of using a twin screw extruder, or the like can be preferably employed. From the viewpoint of uniformly dissolving the high molecular weight product, a method of first dissolving the component A which is a high molecular weight product is preferable. In particular, in the case of producing a carbon fiber precursor, the dissolved state of the high molecular weight component A is extremely important, and even if a slight amount of undissolved material exists, it is recognized as a foreign substance. Voids may be formed inside the carbon fiber.

  Specifically, the polymer concentration of the component A with respect to the solvent, that is, when assuming a solution consisting only of the component A and the solvent, the polymer concentration of the component A in the solution is preferably 0.1 to 5% by weight. Then, the B component is mixed, or the monomers constituting the B component are mixed and polymerized. The polymer concentration of the component A is more preferably 0.3 to 3% by weight, and further preferably 0.5 to 2% by weight. More specifically, the polymer concentration of the component A is preferably a quasi-dilute solution in which the polymers are slightly overlapped as an aggregate state of the polymer, and the component B is mixed or the component B is mixed. When the constituent monomers are mixed and polymerized, the mixed state is likely to be uniform, so that a dilute solution that is in an isolated chain state is a more preferable embodiment. The concentration of the dilute solution is considered to be determined by the intramolecular exclusion volume determined by the polymer molecular weight and the solubility of the polymer in the solvent. Less likely to agglomerate and become foreign matter. When the polymer concentration exceeds 5% by weight, an undissolved product of component A may be present. When the polymer concentration is less than 0.1% by weight, it is effective because it is a dilute solution depending on the molecular weight. Is often saturated.

  As described above, the polymer concentration with respect to the solvent of the component A is preferably 0.1 to 5% by weight, and then the method of mixing and dissolving the component B may be used. It is preferable to employ a method of mixing a product obtained by diluting a product with a solvent and a monomer constituting the component B and mixing the monomers by solution polymerization.

  The method for adjusting the polymer concentration of the component A to the solvent to 0.1 to 5% by weight may be a method using dilution or a method using polymerization. When diluting, it is important to stir until it can be diluted uniformly, and the dilution temperature is preferably 50 to 120 ° C. The dilution time varies depending on the dilution temperature and the concentration before dilution, and may be appropriately set. When the dilution temperature is less than 50 ° C, it may take time to dilute, and when it exceeds 120 ° C, the component A may be altered. In addition, from the viewpoint of reducing the process of diluting the overlapping of the polymers and mixing them uniformly, from the production of the A component to the start of mixing of the B component, or the polymerization of the monomer constituting the B component. Meanwhile, the polymer concentration with respect to the solvent of the component A is preferably controlled in the range of 0.1 to 5% by weight. Specifically, when the component A is produced by solution polymerization, the polymerization is stopped when the polymer concentration is 5% by weight or less, and the component B is mixed therewith, or the monomer constituting the component B is mixed. This is a method of polymerizing the monomer. Usually, when the ratio of the charged monomer to the solvent is small, it is often difficult to produce a high molecular weight product by solution polymerization, so the ratio of the charged monomer is increased. At the stage of 5% by weight or less, the polymerization rate is low and a large amount of unreacted monomer remains. The B component may be mixed after removing the unreacted monomer by volatilization, but from the viewpoint of omitting the process, it is preferable to solution polymerize the B component using the unreacted monomer.

  The component A preferably used in the present invention desirably has compatibility with PAN, and is preferably a PAN-based polymer from the viewpoint of compatibility. As the composition, AN is preferably 93 to 100 mol%, and copolymerization may be carried out if the monomer copolymerizable with AN is 7 mol% or less, but the chain transfer constant of the copolymerization component is smaller than AN. When it is difficult to obtain the required Mw, it is preferable to reduce the amount of the copolymer component as much as possible.

  Examples of monomers copolymerizable with AN include acrylic acid, methacrylic acid, itaconic acid and their alkali metal salts, ammonium salts and lower alkyl esters, acrylamide and its derivatives, allyl sulfonic acid, methallyl sulfonic acid and Those salts or alkyl esters can be used. Moreover, it is preferable that A component is substantially linear PAN, and it is preferable not to use the monomer etc. which have a polyfunctional vinyl group. The branching and cross-linking structure is simply determined by whether the relationship between the molecular weight and the radius of rotation obtained by the gel permeation chromatography method-multi-angle light scattering photometry (GPC-MALLS) method is the same as that of linear PAN. I can judge. Those having a crosslinked structure by a covalent bond, a hydrogen bond, or an ionic bond tend to have a smaller radius of rotation than the molecular weight, and are not included in the linear PAN in the present invention.

  The polymerization method for producing the PAN-based polymer as component A can be selected from a solution polymerization method, a suspension polymerization method, an emulsion polymerization method, etc., and the purpose of uniformly polymerizing AN and copolymer components It is preferable to use a solution polymerization method. In the case of polymerizing using the solution polymerization method, as the solvent, for example, a solvent in which PAN is soluble, such as an aqueous zinc chloride solution, dimethyl sulfoxide, dimethylformamide, and dimethylacetamide, is preferably used. If it is difficult to obtain the required Mw, a solvent having a large chain transfer constant, that is, a solution polymerization method using a zinc chloride aqueous solution or a suspension polymerization method using water is also preferably used.

  As the composition of the PAN-based polymer, which is the B component suitably used in the present invention, AN is preferably 93 to 100 mol%, and a monomer copolymerizable with AN is copolymerized if it is 7 mol% or less. However, as the amount of the copolymerization component increases, molecular breakage due to thermal decomposition at the copolymerization portion becomes more prominent in the flameproofing step, and the tensile strength of the resulting carbon fiber decreases.

  Examples of the monomer copolymerizable with AN include, for example, acrylic acid, methacrylic acid, itaconic acid and alkali metal salts thereof, ammonium salts and lower alkyl esters, acrylamide and derivatives thereof, allyl, from the viewpoint of promoting flame resistance. Sulfonic acid, methallylsulfonic acid and their salts or alkyl esters can be used.

  The polymerization method for producing the B component PAN-based polymer can be selected from a solution polymerization method, a suspension polymerization method, an emulsion polymerization method, and the like. It is preferable to use a solution polymerization method. In the case of polymerizing using the solution polymerization method, as the solvent, for example, a solvent in which PAN is soluble, such as an aqueous zinc chloride solution, dimethyl sulfoxide, dimethylformamide, and dimethylacetamide, is preferably used. Among these, dimethyl sulfoxide is preferably used from the viewpoint of PAN solubility. The raw materials used for these polymerizations are preferably used after passing through a filter medium having a filtration accuracy of 1 μm or less.

  The aforementioned PAN-based polymer is dissolved in a solvent in which the PAN-based polymer is soluble, such as dimethyl sulfoxide, dimethylformamide, and dimethylacetamide, to obtain a spinning solution. In the case of using solution polymerization, if the solvent used for polymerization and the spinning solvent are the same, a step of separating the obtained PAN-based polymer and re-dissolving in the spinning solvent becomes unnecessary.

  The polymer concentration in the spinning solution is preferably in the range of 5 to 30% by weight, more preferably 14 to 25% by weight, and most preferably 18 to 23% by weight. If the polymer concentration is less than 5% by weight, the amount of solvent used increases, and the amount of spinning solution discharged from the single die hole increases, which may make it difficult to increase the spinning draft in setting spinning conditions. On the other hand, when the polymer concentration exceeds 30% by weight, the entanglement increases, the molecular weight between the entanglements decreases, and the spinnability may decrease. The polymer concentration of the spinning solution can be adjusted according to the amount of solvent used.

  In the present invention, the polymer concentration is the weight percent of the PAN polymer contained in the PAN polymer solution. Specifically, after weighing the PAN-based polymer solution, the measured PAN-based polymer solution is removed to a solvent that does not dissolve the PAN-based polymer and is compatible with the solvent used for the PAN-based polymer solution. After solvent, the PAN polymer is weighed. The polymer concentration is calculated by dividing the weight of the PAN polymer after desolvation by the weight of the PAN polymer solution before desolvation.

  Further, the viscosity of the spinning solution at a temperature of 45 ° C. is preferably in the range of 15 to 200 Pa · s, more preferably in the range of 20 to 150 Pa · s, and more preferably in the range of 30 to 100 Pa · s. Most preferably. When the solution viscosity is less than 15 Pa · s, since the formability of the spun yarn is lowered, the speed at which the yarn taken out from the die is taken, that is, the spinnability tends to be lowered. Further, when the solution viscosity exceeds 200 Pa · s, the entanglement increases and the molecular weight tends to decrease. The viscosity of the spinning solution can be controlled by the weight average molecular weight, the polymer concentration, and the type of solvent.

  The viscosity of the PAN polymer solution at a temperature of 45 ° C. can be measured with a B-type viscometer. Specifically, the PAN-based polymer solution placed in a beaker is immersed in a hot water bath adjusted to a temperature of 45 ° C. to adjust the temperature, and as a B-type viscometer, for example, B8L manufactured by Tokyo Keiki Co., Ltd. Using a viscometer, rotor No. 4 is used, and the viscosity of the PAN polymer solution is in the range of 0 to 100 Pa · s. p. m. The viscosity of the PAN-based polymer solution is in the range of 100 to 1000 Pa · s. p. m. Measure with

  Furthermore, it is preferable to use this polymer solution after filtration using a filter having a filtration accuracy of 0.5 to 10 μm.

  In the present invention, a carbon fiber precursor fiber is produced by spinning the spinning solution obtained as described above by a dry and wet spinning method.

In the present invention, the number of holes of the die suitably used may When it is 6000 to 30000 pieces. When the number of holes is less than 6000, productivity is lowered, and in such a state, it is difficult to obtain the effect of the present invention. On the other hand, when the number of holes exceeds 30000, the die becomes too large, and it may be difficult to rectify the coagulation bath liquid of the present invention.

  In the present invention, in order to enhance the spinnability of the spinning solution, the hole shape of the nozzle hole is preferably circular. When the hole shape is circular, the maximum hole diameter of the nozzle hole is 0.06 mm to It is preferably 0.22 mm, and more preferably 0.10 to 0.18 mm. When the hole diameter is less than 0.06 mm, the pressure on the back surface of the die increases, and it is often difficult to increase the discharge linear velocity. When the hole diameter exceeds 0.22 mm, it is difficult to reduce the hole pitch. It becomes difficult to increase the yarn density. What is important is to obtain a fiber having an irregular cross-sectional shape by fusing the spinning solution before solidification by reducing the pore pitch, and the number average pore pitch is 0.3 to 0.9 mm. Yes, preferably 0.4 to 0.6 mm. The hole pitch is the distance between the centers of the nozzle holes. The pitch to the closest spinning hole to one spinning hole is defined as the hole pitch, and the number average of the hole pitches in all the spinning holes is the number average hole pitch. To do. By controlling the hole pitch, it becomes easy to produce a precursor fiber bundle having a single fiber fineness distribution corresponding to about a single hole to 6 holes. When the pore pitch is as small as the range of the present invention, spinnability is lowered and dry-wet spinning is often difficult, but spinning is facilitated by using a spinning solution suitably used in the present invention. .

  In the present invention, the hole diameter of the nozzle hole can be measured by observing the spinneret surface with a microscope.

In the method for manufacturing a precursor fiber bundle of the present invention, preferably the air gap distance (Ha) between the spinneret coagulation bath liquid surface may be set from 1 to 5 mm. When Ha is increased, the discharged spinning solution is easily fused, and the cross-sectional shape of the single fiber in the precursor fiber bundle can be controlled by Ha. If Ha is less than 1 mm, the die immersion caused by the liquid flow in the coagulation bath or the fluctuation of the liquid level due to earthquake is suppressed, and if Ha exceeds 5 mm, the spinning solution is likely to break in the air gap.

  The spinning draft of the spinning solution is preferably in the range of 1-15. Here, the spinning draft refers to a value obtained by dividing the surface speed of a roller having a drive source with which the spun yarn first comes off the die (contacting speed of the coagulated yarn) by the discharge linear velocity from the die. If the spinning draft is less than 1, the diameter of the die hole may have to be reduced in order to obtain the desired fineness of the precursor fiber.

  The coagulation bath used in the present invention includes a PAN polymer solvent such as dimethyl sulfoxide, dimethylformamide, dimethylacetamide, zinc chloride aqueous solution, and sodium thiosulfate aqueous solution used as a solvent in the PAN polymer solution, and so-called coagulation. A mixture of facilitating ingredients is used. As the coagulation accelerating component, those which do not dissolve the PAN-based polymer and are compatible with the solvent used in the PAN-based polymer solution are preferable. Specific examples of the coagulation accelerating component include water, methanol, ethanol, and acetone. However, water does not need to be recovered, and in terms of safety, the amount of coagulation accelerating component necessary for coagulation is small. Most preferably, is used. Conditions such as the solvent concentration and temperature of the coagulation bath may be set according to known conditions.

  In the present invention, after a PAN polymer solution is introduced into a coagulation bath and coagulated to form a coagulated yarn, a carbon fiber precursor fiber is obtained through a water washing step, an in-bath drawing step, an oil agent application step, and a drying step. It is done. Moreover, you may add a dry heat extending process and a steam extending process to said process. The solidified yarn may be directly stretched in the bath without the water washing step, or may be stretched in the bath after removing the solvent by the water washing step. Usually, the stretching in the bath is preferably performed in a single or a plurality of stretching baths adjusted to a temperature of 30 to 98 ° C. The draw ratio at that time is preferably 2 to 8 times, and more preferably 2 to 6 times.

  After the stretching step in the bath, it is preferable to apply an oil agent made of silicone or the like to the stretched fiber yarn for the purpose of preventing adhesion between single fibers. As the silicone oil, it is preferable to use a silicone oil containing a modified silicone such as amino-modified silicone having high heat resistance.

  As the drying step, for example, a drying condition in which a drying temperature is 70 to 200 ° C. and a drying time is 10 seconds to 200 seconds gives preferable results. As an improvement in productivity and an improvement in the degree of crystal orientation, it is preferable to stretch in a heating heat medium after the drying step. As the heating heat medium, for example, air, pressurized steam or superheated steam is preferably used in terms of operational stability and cost, and the draw ratio is usually 1.5 to 4 times.

  From the viewpoint of controlling the degree of crystal orientation of the precursor fiber, the draw ratio after taking the solidification of the present invention is 7 to 15 times, preferably 7 to 10 times. When the draw ratio is less than 7 times, the degree of crystal orientation of the precursor fiber is insufficient. On the other hand, when the draw ratio exceeds 15 times, fluff is likely to occur and it is difficult to increase Vf.

  The carbon fiber precursor fiber bundle of the present invention thus obtained is composed of single fibers of precursor fibers having a specific fiber diameter distribution and a cross-sectional shape.

  In the present invention, the distribution of the fiber diameters of the single fibers constituting the carbon fiber precursor fiber bundle must further satisfy the following three conditions.

  As a first condition, the number average fiber diameter in the range from the maximum fiber diameter in the carbon fiber precursor fiber bundle to a fiber diameter 25% smaller than the maximum fiber diameter is R′1, and other single fibers When the number average fiber diameter is R′2, the fiber diameter ratio R ′ defined by the following formula (3) is 0.1 to 0.7, preferably 0.2 to 0.6. is necessary. The range of R is preferably 0.3 to 0.5.

R ′ = R′2 / R′1 Formula (3)
As a second condition, the carbon fiber precursor fiber bundle for obtaining the carbon fiber of the present invention has R′1 of 6 to 11 μm, preferably 6 to 8 μm. As a third condition, when the number N′2 corresponding to R′2 and the number N′1 corresponding to R′1 are set, the blending ratio defined by N ′ = N′2 / N′1 is 0. 0.5 to 2, preferably 0.8 to 1.2, and more preferably 0.9 to 1.1. In order to obtain the mixing ratio N of the carbon fiber bundle of the present invention, the mixing ratio N ′ of the precursor fiber bundle needs to be in the above range. Moreover, in order to express the effect of effectively improving the fiber content rate, it is preferable that the thin fibers are adjacent to the thick fibers, and the thin fibers are already compared to the thick fibers at the precursor fiber bundle stage. It is preferable that it adjoins. For this purpose, it is preferable to control the fusion of the spinning solution by using a spinneret having different nozzle hole pitches.

  The degree of crystal orientation of the precursor fiber bundle of the present invention is 86 to 91%, preferably 86 to 88%. A carbon fiber having a low degree of crystal orientation has insufficient strand tensile elongation. On the other hand, if the degree of crystal orientation exceeds 91%, fluff is likely to occur.

  The precursor fiber bundle of the present invention is preferably configured by concentrating 3000 or more precursor fibers having the above-described characteristics. Although carbon fiber bundles may be formed by combining less than 3,000 precursor fiber bundles, this is not preferable in terms of economy. The number of single fibers constituting the precursor fiber bundle is more preferably 12,000 or more, and further preferably 24,000 or more.

  The basis weight of the precursor fiber bundle of the present invention is 0.2 g / m or more, more preferably 0.4 g / m or more, and 20 g / m is sufficient. When this basis weight is less than 0.2 g / m, it is not preferable in terms of economy.

  In order to control the roundness of the carbon fiber, the roundness of the cross section of the single fiber constituting the precursor fiber bundle of the present invention is preferably 0.1 to 0.85.

Next, the manufacturing method of the carbon fiber of this invention is demonstrated.
In the present invention, the carbon fiber precursor fiber obtained as described above is flame-resistant in which the carbon fiber precursor fiber is flame-resistant in air at a temperature of 200 to 300 ° C., and the fiber obtained in the flame resistance process is 300 to 800 ° C. Carbon fiber through a preliminary carbonization step of precarbonizing in an inert atmosphere at a temperature of 5 and a carbonization step of carbonizing the fiber obtained in the preliminary carbonization step in an inert atmosphere at a temperature of 1,000 to 3,000 ° C. Can be obtained.

  In the present invention, flame resistance refers to heat treatment in an atmosphere containing 4 to 25 mol% or more of air. Usually, the spinning process and the flameproofing process are discontinuous, but part or all of the spinning process and the flameproofing process may be performed continuously.

  The stretch ratio when making flame resistant is 0.8 to 1.2, preferably 0.9 to 1.1. If the draw ratio at the time of flame resistance is less than 0.8, the tension in the flame resistance process is lowered, and scratching may occur in the flame resistance furnace slits, etc., and the single fiber strength distribution of the resulting carbon fiber is expanded. On the other hand, if the stretch ratio at the time of flame resistance exceeds 1.2, the stretch tension is too high and is pressed by a roller or the like so that an indentation remains or a defect may be enlarged.

  The flameproofing treatment time can be appropriately selected within a range of 10 to 100 minutes. However, for the purpose of improving the production stability of the subsequent preliminary carbonization and the mechanical properties of the resulting carbon fiber, It is preferable to set the specific gravity within a range of 1.3 to 1.38.

  Pre-carbonization and carbonization are performed in an inert atmosphere, and as the inert gas used, for example, nitrogen, argon, xenon, or the like is used. Nitrogen is preferably used from an economical viewpoint.

  In addition, it is preferable that the temperature increase rate in preliminary carbonization is set to 500 ° C./min or less.

  The stretch ratio when performing preliminary carbonization is 0.95 to 1.2, preferably 1.0 to 1.1. When the draw ratio at the time of preliminary carbonization is less than 0.95, the degree of orientation of the resulting preliminary carbonized fiber becomes insufficient, and the strand tensile elastic modulus of the carbon fiber decreases. On the other hand, if the draw ratio during preliminary carbonization exceeds 1.2, the draw tension may be too high and may be pressed by a roller or the like to leave indentations or enlarge defects.

  The carbonization temperature is preferably 1,000 to 2,000 ° C, more preferably 1,200 to 1800 ° C, and still more preferably 1,300 to 1,600 ° C. Generally, the higher the maximum temperature of carbonization, the higher the tensile tensile modulus of the strand, but the tensile strength becomes a maximum at around 1,500 ° C. Therefore, the carbonization temperature is set in consideration of the balance between the two.

  The stretch ratio when carbonizing is 0.96 to 1.05, preferably 0.97 to 1.05, and more preferably 0.98 to 1.03. When the draw ratio at the time of carbonization is less than 0.96, the orientation degree and denseness of the obtained carbon fiber become insufficient, and the strand tensile elastic modulus is lowered. On the other hand, if the drawing ratio during carbonization exceeds 1.05, the drawing tension may be too high and may be pressed by a roller or the like to leave indentations or enlarge defects.

  When a carbon fiber having a higher elastic modulus is desired, graphitization can be performed following the carbonization step. The temperature of the graphitization step is preferably 2000 to 2800 ° C. The maximum temperature is appropriately selected and used according to the required characteristics of the desired carbon fiber. The drawing ratio in the graphitization step is preferably selected as appropriate within a range where no deterioration in quality such as generation of fluff occurs according to the required characteristics of the desired carbon fiber.

  The obtained carbon fiber can be subjected to electrolytic treatment for its surface modification. The electrolytic solution used for the electrolytic treatment includes an acidic solution such as sulfuric acid, nitric acid and hydrochloric acid, an alkali solution such as sodium hydroxide, potassium hydroxide, tetraethylammonium hydroxide, ammonium carbonate and ammonium bicarbonate, or a salt thereof as an aqueous solution. Can be used as Here, the amount of electricity required for the electrolytic treatment can be appropriately selected according to the carbonization degree of the carbon fiber to be applied.

  Electrolytic treatment can optimize the adhesion to the carbon fiber matrix in the resulting fiber reinforced composite material, causing brittle fracture of the composite material due to too strong adhesion and lowering the tensile strength in the fiber direction In addition, although the tensile strength in the fiber direction is high, the adhesive property with the resin is poor, and the problem that the strength characteristics in the non-fiber direction are not expressed is solved, and in the obtained fiber reinforced composite material, in both the fiber direction and the non-fiber direction A balanced strength characteristic is developed.

  After the electrolytic treatment, a sizing treatment can also be applied to give the carbon fiber a bundling property. As the sizing agent, a sizing agent having good compatibility with the matrix resin or the like can be appropriately selected according to the type of resin used.

  The carbon fiber obtained by the present invention is a carbon fiber reinforced composite material excellent in various mechanical properties such as post-impact compressive strength by various molding methods such as autoclave molding as a prepreg and molding by resin transfer molding as a preform such as a woven fabric. Therefore, it can be suitably used as a carbon fiber reinforced composite material having excellent post-impact compressive strength for aircraft structural materials, automotive applications, marine applications, sports applications and other general industrial applications.

  Hereinafter, the present invention will be described more specifically with reference to examples. The measurement method used in this example will be described next.

<Cross-sectional shape of single fiber of carbon fiber>
The carbon fiber bundle was cut with a razor perpendicular to the fiber axis, and the cross-sectional shape of the single fiber was observed using an optical microscope. The measurement magnification was about 200 to 400 times so that the thinnest single fiber was about 1 mm. By analyzing the obtained image, the cross-sectional area and circumference of the single fiber of carbon fiber are obtained, and the cross-sectional diameter (fiber diameter) of the single fiber is calculated from the cross-sectional area in units of 0.1 μm. The roundness of a single fiber was determined using the following formula (2), and its number average value and coefficient of variation were determined. The fiber diameter was determined by obtaining 2000 points, the distribution was evaluated, and the roundness was an average value of 3 single fibers randomly selected from 2000.

Roundness = 4πS / L ² (2)
(In the formula, S represents the cross-sectional area of the single fiber, and L represents the circumference of the single fiber).

<Strand tensile elongation of carbon fiber bundle>
It is determined according to JIS R7608 (2007) “Resin-impregnated strand test method”. The carbon fiber resin-impregnated strand to be measured is 3,4-epoxycyclohexylmethyl-3,4-epoxycyclohexyl-carboxylate (100 parts by weight) / 3 boron trifluoride monoethylamine (3 parts by weight) / acetone (4 parts by weight). ) Is impregnated into carbon fiber or graphitized fiber and cured at a temperature of 130 ° C. for 30 minutes. The number of carbon fiber strands to be measured is 6, and the average value of each measurement result is the tensile strength. In this example, “Bakelite” (registered trademark) ERL4221 manufactured by Union Carbide Co., Ltd. was used as 3,4-epoxycyclohexylmethyl-3,4-epoxycyclohexyl-carboxylate. The n number was 6, and the average value was obtained.

<Crystal orientation degree of precursor fiber>
The degree of orientation in the fiber axis direction was measured as follows. The fiber bundle is cut to a length of 40 mm, and 20 mg is precisely weighed and sampled so that the sample fiber axes are exactly parallel, and then a thickness of 1 mm is uniform using a sample adjusting jig. Sample fiber bundles were arranged. After impregnating with a thin collodion solution and fixing it so as not to lose its shape, it was fixed to a sample table for wide-angle X-ray diffraction measurement. From the half width (H °) of the spread of the profile in the meridian direction including the highest intensity of diffraction observed near 2θ = 17 °, using Cu Kα ray monochromated with a Ni filter as the X-ray source. The degree of crystal orientation (%) was determined using the following formula. The n number was 3, and the average value was obtained.

Crystal orientation degree (%) = [(180−H) / 180] × 100
In addition, Shimadzu Corporation XRD-6100 was used as said wide angle X-ray diffraction apparatus.

<Compression test of fiber reinforced composite material>
The following raw material resins were used and kneaded with a kneader to prepare a resin composition.
Bisphenol A type epoxy resin (Epicoat (registered trademark) 825, manufactured by Japan Epoxy Resin Co., Ltd.): 50 parts by weight, tetraglycidyldiaminodiphenylmethane (ELM434, manufactured by Sumitomo Chemical Co., Ltd.): 50 parts by weight, 15 parts by weight of polyethersulfone resin 4,4′-diaminodiphenylsulfone: 46 parts by weight, nylon 12 particles (manufactured by Toray Industries, Inc., SP500, average particle size 5 μm): 16 parts by weight Preparation of Prepreg For the matrix resin composition, a base resin excluding nylon 12 particles was prepared, and coated on a release paper with a resin basis weight of 21 g / m ² using a knife coater to prepare a resin film. The resin film was superposed on both sides of each example and comparative example carbon fiber (weighing 210 g / m ² ) which were aligned in one direction, and heat matrix was used to impregnate the matrix resin composition while heating and pressurizing. A prepreg was obtained. Next, a matrix resin composition prepared by adding nylon 12 particles so that the final matrix resin composition of the composite material prepreg becomes the above-mentioned blending amount, and is separated at a resin basis weight of 21 g / m ² using a knife coater. A resin film was prepared by coating on a pattern paper. This resin film was superposed on both surfaces of the primary prepreg and a heat roll was used to impregnate the resin while heating and pressing to obtain the desired prepreg.
2. Compression test of fiber reinforced composite material The unidirectional prepreg obtained by the above method was cut into a predetermined size, and after laminating six sheets in one direction, a vacuum bag was formed, and an autoclave was used, the temperature was 180 ° C, Curing was performed for 2 hours under a pressure of 0.59 MPa, and two unidirectional reinforcing materials (fiber reinforced composite materials) were produced.
Four plates in which one fiber-reinforced composite material was cut to 35 × 100 mm in the fiber direction were produced.
These 4 sheets are used as tab materials, and are placed on the other unidirectional reinforcing material so that the distance between the tabs is 8 mm and the distance between the tabs is the same on both sides, and are attached with an adhesive, to JIS K7076 (1991). Test specimens for the method A described were prepared. According to JIS K7076 (1991), this specimen was subjected to a compression test at a crosshead speed of 1.0 mm / min using an Instron universal testing machine (Instron). The number of n of the test piece was 5 and the average value was obtained.

[Example 1]
100 parts by weight of AN, 1 part by weight of itaconic acid, and 130 parts by weight of dimethyl sulfoxide were mixed and placed in a reaction vessel equipped with a reflux tube and a stirring blade. After replacing the space in the reaction vessel with nitrogen to an oxygen concentration of 100 ppm, as a radical initiator, 0.002 part by weight of 2,2′-azobisisobutyronitrile (AIBN) was added, and the following conditions were added while stirring: The heat treatment (referred to as polymerization condition B) was performed.

-Hold at 65 ° C for 2 hours-Decrease in temperature from 65 ° C to 30 ° C (Temperature drop rate: 120 ° C / hour)
Next, 240 parts by weight of dimethyl sulfoxide, 0.4 part by weight of AIBN as a radical initiator, and 0.1 part by weight of octyl mercaptan as a chain transfer agent were weighed and introduced into the reaction vessel, and the following stirring was performed. A heat treatment (referred to as polymerization conditions A) of (1) to (4) was performed and polymerized by a solution polymerization method to obtain a PAN polymer solution.
(1) Temperature increase from 30 ° C to 60 ° C (temperature increase rate 10 ° C / hour)
(2) Hold for 4 hours at a temperature of 60 ° C. (3) Increase the temperature from 60 ° C. to 80 ° C. (Temperature increase rate: 10 ° C./hour)
(4) Hold for 6 hours at a temperature of 80 ° C. Use the obtained PAN-based polymer solution to prepare a polymer concentration of 20% by weight, and then blow ammonia gas until the pH reaches 8.5. Thus, an ammonium group was introduced into the PAN polymer while neutralizing itaconic acid to obtain a spinning solution. The PAN polymer in the obtained spinning solution had Mw of 480,000, Mz / Mw of 5.7, and M _{Z + 1} / Mw of 14, and the spinning solution had a viscosity of 45 Pa · s.

The obtained spinning solution was controlled to a temperature of 3 ° C. by temporarily running a 2 mm air gap from a spinning die having a nozzle diameter of 0.14 mm, a hole pitch of 0.4 mm, and a hole number of 12,000 at a temperature of 40 ° C. Spinning was performed by a dry-wet spinning method introduced into a coagulation bath composed of an aqueous solution of 20% by weight dimethyl sulfoxide to obtain a coagulated yarn. After washing the obtained coagulated yarn with water, it is stretched in hot water at a temperature of 70 ° C. at a stretch ratio of 3 times in a bath, further provided with an amino-modified silicone oil, and dried using a hot drum at a temperature of 190 ° C. Thereafter, the carbon fiber precursor fiber bundle was obtained by performing 2.5-fold post-drawing between two 190 ° C. hot drums. The obtained carbon fiber precursor fiber bundle had almost no fuzz and its quality was excellent. The results of evaluating the properties of the precursor fiber bundle are shown in Table 1.
The obtained precursor fiber bundle was heated in air at 240 to 280 ° C. to be converted into flame resistant fibers. The flameproofing time was 40 minutes, and the stretch ratio in the flameproofing process was 1.00.
Further, the flame-resistant fiber was heated in a nitrogen atmosphere at 300 to 800 ° C. to be pre-carbonized, and then heated in a nitrogen atmosphere at a maximum temperature of 1300 ° C. for carbonization. The stretch ratio in the preliminary carbonization treatment step was 1.0, and the stretch ratio in the carbonization treatment step was 0.97. Furthermore, the fiber obtained by the carbonization treatment was anodized with an electric quantity of 10 coulomb / g-CF in a sulfuric acid aqueous solution to obtain a carbon fiber bundle. Table 1 shows the characteristics of the carbon fiber bundle and the measurement results of the characteristics of the composite material using the carbon fiber bundle.

[Example 2]
A carbon fiber bundle was obtained in the same manner as in Example 1 except that spinning was performed with the height of the air gap being 5 mm.

[Example 3]
A carbon fiber bundle was obtained in the same manner as in Example 1 except that spinning was performed with the height of the air gap being 1 mm.

[Example 4]
A carbon fiber bundle was obtained in the same manner as in Example 1 except that the fiber diameter was changed by adjusting the discharge amount.

[Example 5]
A carbon fiber bundle was obtained in the same manner as in Example 1 except that the fiber diameter was changed by adjusting the discharge amount.

[Comparative Example 1]
A carbon fiber bundle was obtained in the same manner as in Example 1 except that the fiber diameter was changed by adjusting the discharge amount and the coagulation bath concentration was changed to 50% by using a thread cap having a hole pitch of 3 mm. .

[Comparative Example 2]
A carbon fiber bundle was obtained in the same manner as in Example 1 except that the fiber diameter was changed by adjusting the discharge rate using a spinneret having a hole pitch of 3 mm.

[Comparative Example 3]
A carbon fiber bundle was obtained in the same manner as in Example 1 except that spinning was performed with an air gap height of 10 mm. When the cross-section of the composite material was observed, there were voids that seemed to be insufficiently impregnated, and the compressive strength of the composite material was reduced.

[Comparative Example 4]
A carbon fiber bundle was obtained in the same manner as in Example 1 except that spinning was performed with the height of the air gap set to 0.4 mm. When the cross-section of the composite material was observed, there were voids that seemed to be insufficiently impregnated, and the compressive strength of the composite material was reduced.

[Comparative Example 5]
A carbon fiber bundle was obtained in the same manner as in Example 1 except that the fiber diameter was changed by adjusting the discharge amount.

Table 1 summarizes the results of the precursor fiber production conditions and the evaluation thereof in the examples and comparative examples described above.

  In the present invention, it is possible to provide a carbon fiber bundle that can easily improve the physical properties of the entire composite material while improving the physical properties that are likely to decrease at a high Vf, such as compressive strength after impact.

Claims (4)

In the fiber diameter distribution, when the number average fiber diameter in the range from the fiber diameter 25% smaller than the maximum fiber diameter to the maximum fiber diameter is R1, and the number average fiber diameter of other single fibers is R2, When the fiber diameter ratio R defined by the following formula (1) is 0.2 to 0.7, R1 is 4 to 7 μm, the number N2 corresponding to R2, and the number N1 corresponding to R1, N = Mixing ratio defined by N2 / N1 is 0.5-2, strand tensile elongation of the carbon fiber bundle is 1.0-3.0%, and number average roundness of single fiber cross section Is a carbon fiber bundle having a basis weight of 0.1 g / m or more.
R = R2 / R1 Formula (1) In the distribution of the fiber diameter, the number average fiber diameter in the range up to the maximum fiber diameter 25% smaller fiber diameter for a maximum fiber diameter 'is 1, the number-average fiber diameter of other monofilament R' R 2 The fiber diameter ratio R ′ defined by the following formula (3) is 0.2 to 0.7, R ′ 1 is 6 to 11 μm, and the number N′2 corresponding to R′2, When the number N′1 corresponding to R′1 is set, the blend ratio defined by N ′ = N′2 / N′1 is 0.5 to 2, and the yarn crystal orientation is 86 to 91%. A polyacrylonitrile-based carbon fiber precursor fiber bundle having a basis weight of 0.2 g / m or more.
R ′ = R′2 / R′1 Formula (3) The polyacrylonitrile-based polymer solution was dry-wet spinning, a method for obtaining a carbon fiber precursor fiber bundle to a draw ratio after solidification take-up to 7-15 times, the spinneret hole pitch 0.3~0.9mm The number of holes in the die is set to 6000 to 30000, the air gap distance between the spinneret and the coagulation bath liquid surface is set to 1 to 5 mm, and the basis weight of the carbon fiber precursor fiber bundle is 0.2 g / m or more. A method of producing a carbon fiber precursor fiber bundle, wherein spinning is performed by adjusting the discharge amount of the polyacrylonitrile polymer solution . The polyacrylonitrile-based carbon fiber precursor fiber bundle according to claim 2 or the carbon fiber precursor fiber obtained by the production method according to claim 3 is flame-resistant in air at a temperature of 200 to 300 ° C. Flame-proofing step, pre-carbonization step of pre-carbonizing the fiber obtained in the flame-proofing step in an inert atmosphere at a temperature of 300 to 800 ° C., and fiber obtained in the pre-carbonization step of 1,000 to 3, 000 sequentially Ru through the carbonization step of carbonizing in an inert atmosphere at a temperature of ° C., method of producing a carbon fiber bundle.