JP2005194550A - Steel with high strength and excellent cold headability, fastening parts, such as screw and bolt, or formed article, such as shafts, with excellent strength and their manufacturing methods - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide steel which causes neither recess crack nor defects similar to it even if formed into a formed article without heat treatment and has a high level of strength even if refining treatment is omitted. <P>SOLUTION: The steel with high strength and excellent cold headability has a chemical composition containing <0.45 mass% C and a structure having ferritic structure as a primary phase and has mechanical properties of ≥65% reduction of area and ≥600 MPa tensile strength. Further, the steel is free of quenching or quench-and-temper treatment. By using this steel, the formed articles, such as fastening parts and shafts, are obtained. <P>COPYRIGHT: (C)2005,JPO&NCIPI

Description

  The invention of this application includes a steel having a high strength and a high ductility excellent in cold heading, a fastening part such as a screw and a bolt having a high strength manufactured from the steel, or a molded product such as a shaft, and The present invention relates to a manufacturing method thereof, and in particular, clearly defines the material characteristics and metal structure, etc. that each of these steels and molded products should have, and the steel and molded products have the material characteristics and metal structures, etc. The present invention relates to a technology for manufacturing the steel and the molded product.

  Conventionally, hexagon bolts and other relatively high-strength mechanical structural parts manufactured by forming steel wire or steel rod by cold forging, rolling, cutting, etc., improve the cold forging characteristics in advance. In addition, it is necessary to apply a so-called spheroidizing annealing process in which a steel wire or a steel rod is heated at a temperature of about 700 ° C. for a long time from a dozen hours to a whole day and night, and the cementite in the metal structure is spheroidized. In some cases, it is necessary to adjust the material properties by quenching or quenching / tempering. Further, after forming into a machine structural part or the like by cold heading or the like, it is necessary to improve the strength and toughness by performing a tempering treatment such as quenching and tempering. As described above, the manufacturing process of relatively high-strength mechanical structural parts and the like is complicated and requires a plurality of processes. For this reason, there are many heat energy losses, productivity is low, and there are problems in terms of increase in heat treatment costs and delivery time management.

In order to solve the above problems, a technology is proposed that can produce a final product without performing tempering treatment such as quenching and tempering after forming into a product shape by forming including cold heading. Has been. For example, as a material to be used, a steel wire or a steel bar that has been manufactured in the past has a metal structure that has a hardened / tempered structure, and its mechanical property value satisfies a specific condition, that is, yield strength ( YS) and a steel wire or steel bar having a product hardening index (n value) (YS × n) in the range of 4.0 to 11.0 kgf / mm ² (39.2 to 107.9 MPa). By using this as a raw material, it is not necessary to apply a tempering treatment even after it is cold formed and processed into a product shape. Alternatively, a steel bar has been proposed (Patent Document 1).

According to Patent Document 1, if the product of the yield strength and the work hardening index is in the range of 4.0 to 11.0 kgf / mm ² as described above, a specific V notch In a compression test performed on a test piece having a shape, a critical compression rate (%) is determined for preventing the occurrence of cracks longer than a predetermined length on the bottom surface of the V-notch, and this critical compression rate is a predetermined standard value. In the case of a steel material having excellent strength and toughness exceeding the above, it is proposed that it is not necessary to perform a tempering treatment after cold forging. However, in the technique of Patent Document 1, the steel wire or the steel rod that is a material for cold forging into a hexagon bolt or the like does not require spheroidizing annealing that requires a long time, but cold forging. The need for a short quenching and tempering treatment for the previous steel wire or bar is still not resolved.

On the other hand, it is excellent in cold workability without performing spheroidizing annealing on the wire or bar that is usually performed to improve the cold forging of the wire or bar manufactured by hot rolling. A technology for manufacturing cold forging steel has been proposed (Patent Document 2). That is, by generating C in the steel as a carbide other than Fe ₃ C at a temperature higher than the cementite formation temperature, the amount of solid solution C in the steel is substantially reduced, and the cementite that inhibits deformation resistance and deformability, As a result, while suppressing the formation of pearlite, the amount of pro-eutectoid ferrite is greatly increased, and the cold workability is greatly improved. Specifically, as the chemical component composition, C: 0.06 to less than 0.45 mass%, Si: 0.05 mass% or less, Mn: 0.5 to 1.0 mass%, and V: 0.10 The total amount of pro-eutectoid ferrite and pearlite is 90% or more in area ratio, and the pro-eutectoid ferrite amount is f (%) = 100−125 × C (mass%). + 22.5 × V (mass%) The area% is equal to or greater than the value of f (provided that f = 100% when f> 100%), and VC is precipitated in the pro-eutectoid ferrite. Steel has been proposed. As a method for producing such steel, a steel slab having the above chemical composition is heated at 1000 to 1250 ° C., the finishing temperature is Ar3 or higher, FDTL (° C.) = 800 + 190 × (C (mass%) + 0.5 × Hot rolling is performed at a temperature equal to or less than the value of FDTL represented by V (mass%), and cooling is performed at 1 ° C./s or less after the end of rolling.

According to Patent Document 2, although the spheroidizing annealing treatment can be omitted, the tensile strength of the steel does not reach 500 MPa, so it is compared with a molded product after cold forging of the steel. When high strength is required, tempering may be required. Moreover, since addition of V which is a comparatively expensive alloy element is required, it leads to a cost increase.
JP 2003-113422 A JP 2000-273580 A

  Now, among mechanical parts, screws and bolts such as male screws (set screws, set screws, tapping screws) or wood screws belonging to threaded parts are conventionally hot-worked into steel pieces having a predetermined chemical composition. To produce a steel wire or a steel bar having a predetermined cross-sectional shape, a steel wire or a steel bar is subjected to spheroidizing annealing to improve the formability, a predetermined cold forging and rolling, It is formed into a product shape by cold forging and cutting, or by molding mainly of the cutting process. Next, a predetermined tempering treatment according to the product standard is performed to improve mechanical properties, and a surface treatment is appropriately performed to obtain a product.

  FIG. 11 illustrates a schematic flow diagram of a conventional manufacturing process until a molded product 7 such as a fastening part such as a screw and a bolt or a shaft is manufactured from the steel piece 1 or the like. Here, the chemical composition of the steel slab is regulated to an appropriate one according to a desired product standard. The steel slab 1 is processed into a semi-finished product 3 by hot rolling or hot forging 2a, and then further processed into a steel wire or steel bar 4 by hot rolling or hot forging 2b. Quenching and tempering to improve the strength of the steel wire or steel bar 4 obtained, or formability of the material during cold heading in the next process, for example, preventing cracking during recess molding of the screw head For this purpose, a heat treatment 5 such as spheroidizing annealing is performed to soften the material. In this way, the material provided with the required mechanical properties is formed into fastening parts such as screws and bolts or shafts by cold forging and rolling 6 or the like. In addition, when manufacturing various shafts, it is often formed by the cutting process 25. Therefore, in this case, the yield from the wire or bar to the molded product 7 is extremely reduced, for example, about 60 to 65%.

  Necessary mechanical properties are imparted to the various molded articles 7 thus obtained by further appropriate tempering treatment 8. Next, a surface treatment 9 is appropriately performed to obtain a product 10.

  The cold forging and rolling 6 in the above manufacturing process generally has the characteristics that there is no waste in the amount of material used, the dimensional accuracy of the product is good, the mechanical properties are improved, and the surface roughness is good. . Therefore, particularly in the forming of shafts, if the cold forging process is applied instead of the main part of the cutting process, the forming yield is dramatically improved.

Next, FIG. 12 illustrates a conceptual diagram for explaining a header processing method in the case of forming a head of a small screw by cold heading as an example of a screw. This is an example of a double-stepped header (double header), which is formed by combining one die 11 and two punches 12a and 12b. A steel wire as a raw material is cut to a required length, and the cut steel wire (material) 13 is extruded into a die 11 with a first punch (preliminary upsetting punch) 12a as shown in FIG. Then, primary molding including the head is performed to form a preformed product, and then, as shown in FIG. 4B, a second punch (finish upsetting punch) 12b is extruded to form an outer shape of the screw. At the same time, a recess having a cross shape or the like (a hollow portion having a cross shape or the like for tightening the screw with a screwdriver) is formed on the head 14 of the intermediate molded product 16 in the die 11 by the second punch 12b. FIG. 2C shows an example of a schematic perspective view of an intermediate molded product 17 in which a recess 15 is molded on the head 14. At the time of forming the recess 15, a large deformation process having a complicated shape is applied to the top of the head. For this reason, as a material characteristic of the crown, when high ductility is not provided, cracks or cracks occur in the portion during recess molding. Fastened parts such as screws and bolts or molded parts such as shafts in which the recess cracks have occurred cannot be restored into finished products.

  Therefore, in order to prevent the occurrence of recess cracks in the past, there is a method of limiting the maximum material strength such as softening the steel wire, for example, suppressing the tensile strength to about 500 MPa or less by spheroidizing annealing. It is taken. However, if the strength of the wire (material) is limited in this way, if a screw or the like is formed from the wire having such a material strength, a screw or the like that satisfies the desired mechanical properties, particularly strength, cannot be produced as it is. After forming the threaded part by roll forming after recess molding and forming the outer shape of the screw, etc., after applying tempering treatment such as quenching and tempering, and improving its mechanical properties to the required value The product is sent to the product line and surface treatment such as plating is performed as necessary.

  By the way, the tendency of the occurrence of the recess crack is generally increased as the strength or hardness of the material is large and the material is not excellent in ductility. Therefore, even if it is used in applications involving such recess forming, recess cracks do not occur, and it is not necessary to apply tempering treatment such as quenching and tempering after the thread rolling In addition to having a high level of ductility, it is an essential requirement that the steel wire or the like as the material has a high strength to satisfy the standard of a desired screw or the like.

  Therefore, in the case of manufacturing a fastening part such as a screw and a bolt or a molded product such as a shaft that causes a recess crack or a similar defect, it occurs in the cold forging described above. In order to prevent the occurrence of recess cracks or similar defects, it is possible to increase the cost as the chemical composition of the steel slab 1 shown in FIG. After controlling the manufacturing conditions of the steel wire or the steel rod 4 as the material of the molded product 7 such as the fastening parts such as screws and bolts or shafts, and further forming the threaded portion by rolling or cutting. Tempering treatment 8 such as quenching or nitriding quenching / tempering is applied to improve strength and toughness.

  Also, shafts are currently manufactured in the cold forging process or this and the cutting process, but at present there are many cases where softening annealing is required, and there is a strong demand for their omission.

As described above, spheroidizing annealing is applied at the stage of the steel wire or steel bar (wire or bar), which is the raw material, and this is further processed after cold forming and rolling or cutting. If quality treatment is applied, energy costs will increase, and the yield will be reduced by cutting, the line will become complicated, the number of manufacturing processes will increase, making it difficult to shorten the production delivery time, and maintenance costs for the production line. Also rises. However, according to the prior art, as seen in the technique of Patent Document 1, after being formed into a bolt or the like by cold heading, it can be used for the intended application without being subjected to a tempering treatment. In addition, the steel wire or bar is subjected to quenching and tempering, which is more advantageous in the manufacturing process than spheroidizing annealing, which takes a long time, and the obtained wire or bar has a material parameter: yield strength and Product with work hardening index (YS × n) is 4.0-11.0k
The technique of using the thing in the range of gf / mm < ² > (39.2-107.9MPa) is disclosed. However, the technique of Patent Document 1 still requires a quenching / tempering process at the stage of the steel wire or the steel bar. It is also questionable whether there is a clear relationship between the parameter (YS × n) and the occurrence of recess cracks or similar defects. The reason is that the parameter (YS × n) is a parameter representing yield strength and work-hardening balance, whereas the non-occurrence requirement for recess cracks or similar defects is represented by a parameter representing ductility. This is because the inventors of this application have newly found out that it is.

  Furthermore, since there are various types of recesses, steel, wire, or rods for suppressing the occurrence of recess cracks or similar defects are also various depending on the specified strength level of product standards such as screws. A material having a strength of the above level is required, and a material excellent in cold heading is required.

  On the other hand, with the technique of Patent Document 2, a steel excellent in cold heading property that does not require spheroidizing annealing after being processed into a steel wire or a steel rod is obtained for the production of high-strength screws and the like. However, there is a limit to the strength level. For example, the tensile strength is about 440 MPa according to the same document (Example, Table 3), and it is satisfactory as a material such as a screw that requires various higher strength levels. Can not.

  Therefore, in the invention of this application, after being processed into a steel wire or a steel bar, a fastening part such as a screw and a bolt or the like by cold forging and rolling or cutting or cutting main processing without being subjected to heat treatment or Even if it is molded into molded parts such as shafts, recess cracks or similar defects do not occur, and it is possible to adjust to molded parts such as screws and bolts or shafts after molding by cold forging. Without any quality treatment, the present invention provides a wire or bar that already has a desired high level strength at the stage of a steel wire or bar, and a steel containing the bar or wire in a wide range. PROBLEM TO BE SOLVED: To provide a molded product such as a high-strength screw and bolt and other fastening parts or shafts using a bar or steel, and further to provide a method of manufacturing these wire or bar or steel, and a molded product It is said.

  In the following description of the invention, the steel wire or steel bar refers to the one that is still rolled or the like, and the wire or bar is the following regardless of whether or not a tempering treatment is applied in a broad sense. A material (material) having an appropriate material characteristic to be supplied as a molding material in the process shall be indicated.

  In order to solve the above-mentioned problems, the inventors of this application conducted extensive research. First, the inventors have determined whether the wire, rod, or steel to be provided by the present invention must satisfy the conditions in terms of chemical composition, metallographic structure, and mechanical properties. investigated. As a result, first of all, regarding the chemical composition, C: 0.45% by mass, and regarding the mechanical properties, the tensile strength meets the standard of the final product type that is the production target. In the invention, the precondition is that the tensile strength is 600 MPa or more, and on that basis, a particularly important factor is the level of drawing, and the drawing of the material needs to be 65% or more. I found out that there was. Further, it was found that it would be more desirable to obtain a material having a higher tensile strength of 800 MPa or more and a drawing satisfying 70% or more. The inventors have found that the main phase of the metal structure needs to be ferrite in order to provide the steel with such mechanical properties.

In addition, advantageous conditions for having the above-mentioned conditions of having the metal structure and mechanical properties were studied. As a result, in order to obtain a tensile strength of 600 MPa or more, the ferrite structure should be an ultrafine grain steel having an average grain size of ferrite of 2 μm or less in a cross section perpendicular to the rolling direction, and more preferably the average grain size. Has been found to be extremely effective when the thickness is 1 μm or less. As described above, it is important that the diaphragm has a high level among the mechanical properties, and it is not yet known that the value needs to be 65% or more.

  And the important condition of the effective method for producing the steel having the above-mentioned metal structure and mechanical properties is that the total reduction of a predetermined value or more in the warm region within the predetermined temperature range with respect to the steel slab or the steel material. It has been found that a reduction to an area ratio is applied or an average plastic strain of a predetermined value or more is introduced. However, here, warm rolling, and further warm processing, refers to rolling or rolling within a temperature range of 350 to 800 ° C, and rolling or processing at a temperature exceeding this temperature range is hot rolling. Also called hot working. The same applies to the following description.

  The invention of this application has been completed based on the above findings. The summary is as follows.

  Steel having high strength and excellent cold forging according to the invention of claim 1 is C: less than 0.45% by mass of the chemical composition, having a ferrite structure as a main phase, It has a mechanical property of 65% or more and a tensile strength of 600 MPa or more, and is characterized by being not subjected to quenching or quenching / tempering treatment.

  Steel having high strength and excellent cold forging according to the invention of claim 2 has a chemical composition of C: less than 0.45% by mass, having a ferrite structure as a main phase, It has a mechanical property of 70% or more and a tensile strength of 800 MPa or more, and is characterized by being not subjected to quenching or quenching / tempering treatment.

  A steel having high strength and excellent cold forging according to the invention described in claim 3 is the invention described in claim 1 or claim 2, wherein the ferrite structure has a cross section perpendicular to the rolling direction. Is characterized by having a ferrite particle size of 2 μm or less.

  Here, the shape of the ferrite constituting the main phase of this steel is such that when the steel is rolled in a low temperature region of the warm rolling temperature range, for example, 500 ° C., equiaxed grains and elongated grains are mixed. There is. Even if this mixed state exists, there is no problem in the present invention. Even in such a case, the average grain size of the ferrite may be obtained by obtaining the average grain size in a cross section perpendicular to the rolling direction. Further, the steel having ferrite as the main phase means that the second phase may be present as the balance, or that the second phase may not be present and only the ferrite may be present.

  As far as the high-strength steel according to the present invention is concerned and the steel is excellent in cold forging, the shape and grain size of the ferrite grains constituting the main phase of the steel and the presence state of the second phase of the steel are as follows: The same is true below this.

  The steel having high strength and excellent cold forging according to the invention described in claim 4 is the invention described in claim 1 or claim 2, wherein the ferrite structure has a cross section perpendicular to the rolling direction. It has a feature that the average particle diameter of the ferrite has a ferrite particle diameter of 1 μm or less.

  The steel according to the invention described in claim 5 having high strength and excellent cold forgeability is further characterized in that the spheroidizing annealing treatment is further performed in the invention described in any one of claims 1 to 4. It is characterized by not being performed.

A steel having high strength and excellent cold forgeability according to the invention of claim 6 is the invention according to any one of claims 1 to 5, wherein the steel has the following chemical composition, That is, C: 0
. Less than 45% by mass, Si: 2.0% by mass or less (not including 0% by mass), Mn: 3.0% by mass or less (not including 0% by mass), P: 0.2% by mass or less (0% by mass) %), S: 0.03% by mass or less, Al: 0.1% by mass or less (excluding 0% by mass), and N: 0.02% by mass or less, with the balance being Fe and inevitable impurities It is characterized by comprising.

  Here, among the above chemical components, in the present invention, since S and N are both impurities, they may be substantially 0% by mass, but Si, Mn and Al are components to be included, The content of these components does not include 0% by mass. P has the effect of improving the strength, but on the other hand, it deteriorates ductility, particularly the aperture, so the lower one is desirable and may be 0% by mass.

  A steel having high strength and excellent cold forging according to the invention described in claim 7 is the invention described in any one of claims 1 to 6, further excluding the main phase of the steel. The remainder, that is, the second phase is characterized in that the metal structure is mainly composed of cementite, and the remainder consists of at least one of pearlite, martensite, bainite, and a mixture of martensite and austenite. is there.

  The steel having high strength and excellent cold forging according to the invention described in claim 8 is the invention described in any one of claims 1 to 6, further excluding the main phase of the steel. The remainder, that is, the second phase is characterized in that its metal structure is composed of cementite.

  A steel having high strength and excellent cold forging according to the invention described in claim 9 is the invention described in any one of claims 1 to 8, further excluding the main phase of the steel. The remainder, that is, the second phase fraction is 2% by volume or less (including 0% by volume), and is characterized by a multiphase or single phase structure.

  Here, the metal structure of the steel having high strength and excellent cold forging may consist of only a ferrite phase, that is, the fraction of the second phase may be 0% by volume. In addition, although the fraction of the second phase is volume%, in actual measurement, as a simple method, evaluation may be performed by area% on the sample cut surface. The same applies hereinafter.

  A steel having high strength and excellent cold forging according to the invention of claim 10 is the invention according to any one of claims 1 to 9, wherein the steel further has a temperature of 350 to 800 ° C. In this range, the material is produced by rolling the material.

  A steel having high strength and excellent cold forging according to the invention of claim 11 is the invention according to any one of claims 1 to 9, wherein the steel further has a temperature of 400 to 600 ° C. In this range, the material is produced by rolling the material.

  The steel having high strength and excellent cold forging according to the invention of claim 12 is the plasticity of the invention according to claim 10 or 11, further introduced into the material by the rolling and remaining. The strain is characterized in that the average plastic strain into the material calculated by the three-dimensional finite element method is 0.7 or more.

  The steel of high strength and excellent cold forging according to the invention of claim 13 is the invention of any one of claims 10 to 12, wherein the steel is further added to the material. On the other hand, it is characterized in that the plastic strain is introduced into the material by multi-pass rolling in multiple directions.

  Here, rolling the material in multiple directions is based on the orientation of the material immediately before the first pass rolling, and for this material, two or more on a plane perpendicular to the length direction of the material. It means rolling in the direction. For example, as an example when the cross-sectional shape perpendicular to the length direction of the material is a square shape, the material is rolled in two directions, a vertical direction and a horizontal direction perpendicular to the length direction of the material. means. In addition, when the material is rolled in multiple directions, rolling of two or more passes, that is, multi-pass rolling is performed. In the invention of this application, performing multi-pass rolling in multiple directions means the above.

  As described above, the inventions according to claims 1 to 13 are steels having high strength and excellent cold forgeability according to the invention as described above. The steel may be any of wire, bar, plate, etc. regardless of its shape. On the other hand, the inventions of claims 14 to 16 described below are formed parts such as screws and bolts, such as screws and bolts, or shafts having excellent strength according to the invention of this application, and the characteristics thereof will be described below. .

  A molded product such as a fastening part such as a screw and a bolt or a shaft or the like excellent in strength according to the invention described in claim 14 is characterized by being a molded product from any of the steels of claims 1 to 13. Is.

  Here, the fastening parts according to the present invention refer to nuts, rivets, stud bolts, fasteners, and other parts for mechanical structures having functions similar to these in addition to screws and bolts, and shafts are It refers to various shafts such as shafts provided as machine structural parts. The definitions of these terms are all the same in the following description of the present invention.

  A fastening part such as a screw and a bolt excellent in strength according to the invention described in claim 15 or a molded product such as a shaft is manufactured by a processing method including forging using a wire or a bar. It is what you have.

  The fastening parts such as screws and bolts having excellent strength according to the invention described in claim 16 or molded products such as shafts are not further tempered in the invention of claim 14 or 15. It has the characteristics.

  Next, the characteristics of the steel manufacturing method according to claims 17 to 25 according to the present invention, which is high in strength and excellent in cold heading, will be described.

The method for producing a steel having high strength and excellent cold forging according to the invention of claim 17 is a method for producing steel by warm caliber rolling on a steel slab or steel containing C: less than 0.45% by mass. The manufacturing method is as follows. The rolling temperature is set within the range of 350 to 800 ° C., and the formula (1) of the steel slab or steel material in this rolling: R = {(S ₀
-S) / S ₀ } × 100 (where R is the total area reduction (%), S ₀ is the cross-sectional area in the C direction of the steel slab or steel just before the start of rolling, and S is the C direction of the steel obtained after the end of rolling) The total area reduction ratio R expressed by the sectional area is characterized by rolling at 50% or more.

Here, the steel having high strength and excellent cold forgeability is a steel having at least the material characteristics described in claim 1, that is, containing C: less than 0.45 mass%, and mainly having a ferrite structure. Steel having mechanical properties with a tensile strength of 600 MPa or more and a drawing of 65% or more as a phase, or steel having the material properties described in claim 2, that is, C: less than 0.45 mass% Means a steel having a mechanical property of having a ferrite structure as a main phase, a tensile strength of 800 MPa or more and a drawing of 70% or more. The above description applies to all the descriptions relating to the “method for producing steel having high strength and excellent cold forging” according to the present invention according to the present specification.

The method for producing steel having high strength and excellent cold forging according to the invention described in claim 18 is characterized in that C: a steel slab or steel material containing less than 0.45% by mass, by warm caliber rolling in steel. The manufacturing method is as follows. In this rolling, the caliber rolling is performed at a rolling temperature in the range of 350 to 800 ° C., and includes one or more passes using an oval-shaped hole mold and one or more paths using a square or round hole mold. Formula (1) of the above steel slab or steel material: R = {(S ₀ −S) / S ₀ } × 100 (where R is the total area reduction rate (%), S ₀ is the steel slab or steel material immediately before the start of rolling) (C is a cross-sectional area in the C direction, and S is a cross-sectional area in the C direction of the steel obtained after the end of rolling).

The method for producing steel having high strength and excellent cold forging according to the invention described in claim 19 is the material according to claim 18, further comprising a material after rolling using the oval-shaped hole mold. The maximum minor axis length of the cross section in the C direction (pointing to 2A ₀₁ in FIG. 6A described later) is the opposite side of the material in which the cross section in the C direction immediately before rolling using this oval-shaped hole is square It is characterized by being 70% or less of the length (pointing to 2A ₀ in FIG. 6B described later).

  Here, “immediately before rolling using an oval-shaped hole mold” means that only one pass rolling is performed using an oval-shaped hole mold having a certain shape, and two or more oval-shaped hole molds having different shapes are used. When a continuous rolling pass is used, when the same oval shape is continuously carried out twice or more times (so-called through), and a rolling pass in which both are mixed is performed. In any case, it means immediately before the first rolling pass in these continuous rolling passes.

  The method for producing a steel having high strength and excellent cold forging according to the invention of claim 20 is characterized in that C: a steel slab or steel material containing less than 0.45% by mass, by warm caliber rolling in steel. An average plastic strain in a material in which the plastic strain to be introduced into the material by the caliber rolling and the residual plastic strain is calculated by a three-dimensional finite element method is a manufacturing method in which the rolling temperature is in a range of 350 to 800 ° C. The steel slab or the steel material is rolled so as to be 0.7 or more.

  The method for producing a steel having high strength and excellent cold forging according to the invention of claim 21 is a method for producing steel by warm caliber rolling on a steel slab or steel containing C: less than 0.45% by mass. A manufacturing method, in which the rolling temperature is in the range of 350 to 800 ° C., and the following formula (2): Z = log [(ε / t) exp {Q / (8.31 (T + 273))}] (provided that , Ε is the average plastic strain, t is the time (s) from the start to the end of rolling, Q is a constant, 254,000 J / mol, T is the rolling temperature (° C.), and the average temperature of each pass is the temperature It is characterized by rolling so that the rolling condition parameter Z represented by (A) is 11 or more. Here, the value calculated by the three-dimensional finite element method can be used as the average plastic strain ε in the above equation (2).

  The method for producing a steel having high strength and excellent cold forging according to the invention of claim 22 is the invention according to any one of claims 17 to 21, and further in the warm condition. The caliber rolling is characterized by being performed in multiple passes in multiple directions.

  A method for producing steel having high strength and excellent cold forging according to the invention described in claim 23 is the invention according to any one of claims 17 to 22, wherein the steel slab or the steel material is further rolled by 400. It is characterized in that it is carried out within a range of ˜600 ° C.

The method for producing a steel having high strength and excellent cold forging according to the invention described in claim 24 is the invention described in claim 23, and further relates to the rolling temperature of the steel slab or steel material. Is in the range of 400 to 600 ° C., and the material temperature T _{X, out at} the rolling exit of the X pass (where X is a natural number) is 30 ° C. or more higher than the rolling set temperature T _X of the X pass. If this is the case, do you wait until the material temperature T _{X + 1, in} at the rolling entrance of the (X + 1) th pass, which is the next rolling pass, becomes T _{X + 1, in} ≦ (T _X +30) ° C. Or the material is cooled and the rolling is continued.

  The method for producing a steel having high strength and excellent cold forging according to the invention described in claim 25 is the method according to any one of claims 17 to 24, wherein the rolling in the warm is further performed. The steel obtained by this rolling is characterized by not being subjected to spheroidizing annealing.

  Finally, the characteristics of the manufacturing method of a molded part such as a fastening part such as a screw and bolt or a shaft excellent in strength according to the present invention will be described.

  A manufacturing method of a molded part such as a fastening part such as a screw and a bolt or a shaft or the like excellent in strength according to the invention described in claim 26 was obtained by manufacturing the steel of any one of claims 17 to 25. The wire or bar is subjected to processing including forging and molded to produce a molded product according to the present invention.

  Here, “manufacturing wire or bar according to steel manufacturing method” means that the wire or bar of the present invention is included in the steel category of the present invention, that is, the component of the steel. Since it is one, this wire or bar originates from the fact that it can be produced according to this steel production method.

  A method for manufacturing a fastening part such as a screw and a bolt having excellent strength or a molded product such as a shaft according to the invention as set forth in claim 27 is the invention according to claim 26, wherein at least one of the manufacturing methods is included in the entire manufacturing process. It is characterized in that at least one of a forging method and a pressing method is used in place of the rolling method of the part process.

  The manufacturing method of a molded product such as a fastening part such as a screw and a bolt or a shaft or the like excellent in strength according to the invention of claim 28 is molded into the molded product in the invention of claim 26 or claim 27. In any subsequent manufacturing process, the molded product is not subjected to a tempering treatment.

  According to the invention of this application, the facility cost and the running cost are lower than before, and the process management is improved by the simplified production line. In particular, in the molded products of shafts, the molding process yield can be dramatically improved. The present invention provides a high-strength and cold-forgeable steel that can further contribute to energy saving, and a molded part such as screws and bolts, such as screws and bolts that are excellent in strength, or shafts, and a method for producing these. This can provide a very beneficial industrial effect.

Next, the reason for limitation of the aspect in the embodiment will be described together with the embodiment of the invention.
[1] Steel according to the present invention, and fasteners such as screws and bolts according to the present invention or molded products such as shafts, etc., “steel etc.” according to the present invention, and screws and An embodiment of a fastening part such as a bolt or a molded product such as a shaft will be described. Here, “steel etc.” according to this invention is
It is a collective term for “steel” according to the present invention and “wire or rod” used as a material for a fastening part such as a screw and bolt or a molded product such as a shaft according to the present invention. The “steel” and the “wire or bar” are not completely identical, and “steel” includes the “wire or bar”. However, the “steel” and the “wire or rod” have the same chemical composition, metal structure, material properties and the like to be provided. Therefore, in the description in this specification, both are collectively referred to as “steel etc.”.

[1-1] “Steel, etc.” according to the present invention
First, embodiments of the metal structure and material properties that the “steel etc.” according to the present invention should have will be described. The steel according to the present invention is a steel having a high strength and a high ductility, which has high strength and excellent cold forgeability, and has both the form of the metal structure and the characteristics of the mechanical properties as described above. It is based on quantitative definition, and as a desirable embodiment thereof, the ferrite grain size and chemical composition of the steel, etc. are defined within suitable ranges, and the second phase of the metal structure Is preferably defined. Further, a characteristic manufacturing history of the steel or the like is additionally defined. This will be specifically described below.

(1) [C: 0.45 mass%]
C: Less than 0.45% by mass C contributes to improving the strength of the steel. Therefore, it is desirable that the C content is substantially contained in order to secure the strength, but it may be 0. However, when the C content is excessive, the fraction of the second phase of steel or the like whose main layer is ferrite becomes excessive, and the aperture is reduced. In order to secure the aperture at 65% or more, it is necessary that the C content is less than 0.45% by mass. In the case of Si—Mn based carbon steel, if the C content is 0.15% by mass or less, the fraction of the second phase is approximately 2% by volume or less, which is further advantageous from the viewpoint of ensuring ductility. In order to preferentially secure the cold heading properties of steel or the like according to the present invention, drawing characteristics are particularly important. On the other hand, as an important means for ensuring the strength, in addition to the adjustment of the C content, it can be performed by controlling the ferrite grain size of the main phase. In this respect, the C content is more preferably 0.01 to less than 0.45% by mass.

P: 0.2% by mass or less P has an effect of deteriorating ductility. In the steel according to the present invention, it is preferable that the upper limit of the P content is limited to 0.1% by mass so as not to deteriorate the drawing RA, which is extremely important as an index of cold heading.

  In addition, when steel materials are warm-rolled, it can be considered that the chemical component composition of both does not change substantially between the steel materials before rolling and the steel materials after rolling (warm-rolled materials). Also in this invention, the chemical component composition of `` molded product '' such as fastening parts such as screws and bolts or shafts according to the present invention, and the chemical component composition of `` wire or rod '' which is a material of the molded product, It may be considered substantially the same. This applies not only to the item (1) above, but also to the item (5) described later and the item (2) [chemical component composition] in the item [1-2].

(2) [drawing: 65% or more, tensile strength: 600 MPa or more] or
[Drawing: 70% or more, tensile strength: 800 MPa or more]
The steel and the like according to the invention of this application is a machine part that requires relatively strong use, and particularly has high strength and is excellent in cold heading that can withstand severe forming processes. Therefore, it is necessary to use steel having a good balance between high strength and high ductility. The strength level is set to 600 MPa or more in terms of tensile strength, and the ductility level is specified to be 65% or more by drawing. In order to ensure excellent ductility, a high elongation or drawing value is generally an important factor. However, when a material having a high tensile strength of 600 MPa is deformed by cold forging and is subjected to molding under severe conditions, for example, JIS standard M1.6 (Nominal of screw) (Diameter: 1.6 mm) When a recess is cold-formed on the top of the head of a pan head screw with a strength class of 6.8 or more, the ductility level effective for preventing the occurrence of recess cracking is 65% for material drawing. The above is necessary. In this case, the inventors first found out that there is no good correlation between the occurrence of the recess crack and the elongation of the material, and it is difficult to predict the occurrence of the crack with the value of the elongation of the material. FIG. 1 shows such an example. A test in which the total area reduction ratio R is 90% or more by multi-pass rolling in multiple directions in a warm temperature range for a Si—Mn based carbon steel material. In the graph showing the relationship between tensile strength and elongation by tensile test of test materials in, results of no cracking (○ mark) and presence (× mark) during recess forming by cold heading of M1.6 pan head screw It is a figure which shows an example. Further, when a material with higher material strength is required and a tensile strength of 800 MPa or more is required (for example, when the strength classification is 8.8 or more with a JIS standard M1.6 pan head screw), the above-mentioned is required. In order to ensure such cold heading, it is desirable that the drawing be 70% or more. However, the recess shape of the machine screw is not always constant. Therefore, assuming various shapes of recesses, it should be noted that the greater the ratio of the occupied area of the recess to the area of the top surface of the screw, the easier the cracking occurs, and the required strength and drawing level are required. And steel should be designed to be sufficient.

  The above steel having high strength and excellent cold forgeability, that is, steel having high strength and high ductility in a well-balanced manner is indispensable in the following cases. When manufacturing small screws, etc., in order to avoid the occurrence of cold forging cracks such as recess cracks, relatively soft steel is used as the material, the recess is formed by header processing by cold forging, and the threaded portion is rolled. If you want to improve the mechanical properties of the screw by tempering such as quenching or carburizing quenching and tempering after forming, when manufacturing small screws with a screw shaft diameter of 2.0 mm or less Depending on the relationship between the residual stress after quenching or the depth of the carburized layer in the case of carburizing and quenching, and the screw diameter and thread size, heat treatment such as quenching may be difficult. In particular, when the screw shaft diameter is 1 mm or less, or a long screw, it may not be used as a machine part due to deformation accompanying quenching and tempering. In the manufacture of such a micro member, the supply of steel and the like according to the present invention is extremely effective. Further, even if the tempering treatment such as quenching and tempering can be performed as described above, the steel or the like according to the present invention eliminates the need for such a complicated tempering treatment. Great effects such as down and productivity improvement are exhibited.

  In the bolts and small screws specified in the above JIS, the strength classification “8.8” indicates that the left “8” is 1/100 of the tensile strength of 800 MPa, and the right “8” The numerical value is 10 times the ratio of the nominal lowering yield point or nominal yield strength of 640 MPa and the nominal tensile strength of 800 MPa.

(3) [first phase: steel or the like in which the main phase is a ferrite structure, and preferably the ferrite average particle size of a cross-sectional structure perpendicular to the rolling direction is 2 μm or less] or
[First phase: steel etc. in which the main phase is a ferrite structure, and more preferably the ferrite average particle diameter of the cross-sectional structure perpendicular to the rolling direction is 1 μm or less]
In the steel and the like according to the invention of this application, it is an essential requirement that the main phase (first phase) has a double-phase or ferrite single-phase structure composed of ferrite grains as a form of the metal structure of the steel or the like. The present inventors have decided to adopt a method of refining crystal grains as a method of realizing high strength of steel or the like without using any strengthening mechanism by phase transformation. At this time, the present inventors have newly found out that securing the drawing of the obtained steel or the like at a high level is a precondition for preventing the occurrence of recess cracking in the cold heading. Therefore, a test of warm multi-directional multi-pass rolling with a large strain introduced was performed on Si-Mn carbon steel (however, the crystal structure of Fe is bcc) with various chemical composition compositions of steel. It was. From this test result, FIG. 2 is obtained by arranging the relationship between the ferrite average particle diameter d and the tensile strength TS.

From the results shown in FIG. 2, the tensile strength of 600 MPa or more is obtained if the steel has a ferrite structure whose average grain size of the cross-sectional structure perpendicular to the rolling direction is 2 μm or less. If the steel has a ferrite phase with a diameter of (0.7 to 1) μm or less as a main phase, a tensile strength of 800 MPa or more is obtained.

  Furthermore, in the above, even if the grain shape in which the ferrite grains are elongated in one direction is mixed, if the average grain size of the cross-sectional structure perpendicular to the rolling direction is 2 μm or less, the tensile strength TS = 600 MPa or more is obtained. It was also found that when the average grain size of the cross-sectional structure perpendicular to the rolling direction is (0.7 to 1) μm or less, a tensile strength TS = 800 MPa or more can be obtained.

  Next, with respect to the Si-Mn based carbon steel material, the above-described ferrite grain size obtained by a test in which the total area reduction ratio R is 90% or more by multi-pass rolling in multiple directions in the warm temperature range. Plot the relationship between the tensile strength and drawing of the test materials that have the tensile test, while conducting a recess forming test by cold forging M1.6 pan head screws on these test materials to test for the presence of recess cracks. did. The result is shown in FIG. According to FIG. 3, even if the tensile strength is 600 MPa or more, no recess crack occurs if the aperture RA is 65% or more. Furthermore, even though the tensile strength is 800 MPa or more, the drawing RA is further increased to obtain 80% or more of steel, and in this case, there is no recess crack.

  As described above, since there are various types of recesses, the necessary and sufficient conditions that steel or the like should have in order to suppress the occurrence of recess cracks or similar defects are not uniform. It is necessary to consider that recess molding of M1.6 pan head screws requires extremely severe ductility conditions.

  Therefore, in the invention of this application, the test results including FIG. 1, FIG. 2 and FIG. 3 above, considerations for these, and practicality are combined, and M1.6, which requires a very high level of cold forging, is required. The conditions that steels having excellent cold forging properties that can be formed into recesses of various shapes including recesses for pan head screws should have a tensile strength of 600 MPa or more. As a precondition, it was concluded that the drawing RA should be 65% or more. Furthermore, it was found that even for molded products that require a tensile strength of 800 MPa or more, if the drawing RA is 70% or more, cold forging can be performed without cracking even in recesses with considerably severe processing conditions. An advantageous means for providing such a level of tensile strength is that the grain size of the ferrite as the main phase is 2 μm or less in terms of the average grain size of the cross-sectional structure perpendicular to the rolling direction. It has been found that it is effective to make it 1 μm or less.

(4) [Quenching or quenching / tempering treatment unnecessary]
In the steel and the like according to the invention of this application, the main phase (first phase) is composed of ferrite grains, the tensile strength TS is 600 MPa or more, and the drawing RA is 65% or more as the form of the metal structure of the steel or the like. Therefore, it is not necessary to improve the strength and ductility by quenching or quenching / tempering. Further, when the tensile strength TS is 800 MPa or more and the drawing RA is 70% or more, the above heat treatment is further unnecessary.

  Thereby, such a material characteristic as steel according to the present invention exerts a great effect such as omission of a manufacturing process of a fastening part such as a screw and a bolt or a molded product such as a shaft and reduction of manufacturing cost.

(5) [Chemical composition of C]
Furthermore, regarding the chemical composition of the “steel” according to the invention of this application, alloy elements for improving the strength, for example, Cr, Mo, Cu, Ni, without using the strengthening mechanism of the steel by phase transformation. The addition of alloy elements such as Nb, Ti, V and / or B is not an essential requirement. However,
Such alloy elements may be added as appropriate. The steel according to the present invention can be designed with a wide range of chemical composition of ferritic single phase steel. And the desirable range of the chemical component composition excluding C in the chemical component composition of steel or the like according to the invention of this application is as follows.

Si: 2.0% by mass or less (excluding 0% by mass)
Since Si is an element that acts as a deoxidizer, it can reduce the amount of oxide-based non-metallic inclusions remaining in steel and the like, thereby improving cleanliness and contributing to ensuring ductility. In addition, the present inventors have also found that Si is an element that contributes to the improvement of cold heading by an appropriate content. In particular, the effect is exhibited when the Si content is in the range of 0.8 to 1.5 mass%. However, when Si is excessively contained, the ductility is deteriorated on the contrary, and deformation resistance at the time of processing increases. Therefore, the Si content that does not cause ductile deterioration is regulated to 2.0% by mass or less. However, since Si is an element useful in an appropriate content as described above, 0% by mass is not included in the steel according to the present invention.

Mn: 3.0% by mass or less (excluding 0% by mass)
Mn is effective for securing the strength, and contributes to the reduction of oxide-based nonmetallic inclusions remaining in the steel by complex deoxidation with Si. However, when Mn is contained excessively, ductility is deteriorated. Therefore, the upper limit of the Mn content is restricted to 3.0% by mass. In addition, since Mn is a useful element in appropriate content as above-mentioned, in the steel etc. which concern on this invention, 0 mass% shall not be included and it shall be 0.01 mass% or more desirably.

S: 0.03 mass% or less S is an impurity element in the steel and the like according to the present invention, and when the content becomes high, the solid solution S segregates at the grain boundary, and hot from the steel ingot to the steel slab. Since hot workability deteriorates during processing, the content is restricted to 0.03% by mass or less. Further, since it is handled as an impurity element in the present invention, it is desirable that the amount is as small as possible.

Al: 0.1% by mass or less (excluding 0% by mass)
Al is added as a deoxidizer. Moreover, N which segregates at the grain boundary by producing AlN is fixed with Al, and the grain boundary strength is increased. However, if the Al content exceeds 0.1% by mass, the effect is saturated and the surface properties of the steel and the like deteriorate due to the aggregate inclusions of alumina and the like, so the upper limit is made 0.1% by mass. In addition, in order to exhibit the effect as a deoxidizer, the lower limit is desirably 0.005% by mass.

N: 0.02% by mass or less N is not particularly required to be added in the steel according to the present invention, and is handled as an impurity inevitably contained in the melting process. Although it is necessary to consider the balance with the Al content, if it is excessively contained, hot workability is deteriorated due to grain boundary segregation. However, N precipitates as AlN and contributes to refinement of crystal grains. Therefore, it is desirable to limit the upper limit of the N content to 0.02% by mass in consideration of the operability of the melting process. The lower limit value does not need to be regulated considering actual operation.

  In order for the steel and the like according to the present invention to stably exhibit high strength and high ductility with excellent cold forgeability and to reduce manufacturing costs, it is desirable to satisfy all the above-described chemical component compositions. And about Si content, if it adjusts in the range of 0.8-1.5 mass%, the aperture_diaphragm | restriction of steel etc. concerning this invention can be made more excellent.

(6) [Metal structure constituting the second phase: mainly cementite, the balance being one or more of pearlite, martensite, bainite, and a mixture of martensite and austenite, or the entire second phase is cementite], Furthermore,
[Second phase fraction: 2% by volume or less]
Next, in the metal structure of steel or the like according to the present invention, if the main phase is an ultrafine ferrite as described above and has the desired tensile strength and drawing, the second phase is mainly composed of cementite, and the balance May be composed of at least one of pearlite, martensite, bainite, and a mixture of martensite and austenite. Further, the second phase may be composed only of cementite. Furthermore, fine precipitates such as AlN nitride or carbonitride may be contained. The reason is that precipitates such as charcoal and nitride are smaller than cementite and do not deteriorate the aperture. If the fraction of the second phase is 2% by volume or less, the strength and ductility level of the steel, etc. according to the present invention depending on the grain size of the ferrite as the main phase can be secured more stably, which is more desirable. .

  In addition, this steel does not require the use of a steel strengthening mechanism by phase transformation, so various heat treatments are not necessary. From this point of view, energy costs are reduced, and lines are complicated. It is extremely effective in eliminating the increase in the number of manufacturing processes.

(7) [Spheroidizing annealing is not required]
In the “steel etc.” according to the present invention, all of them have the metal structure and mechanical properties as described above, and have high strength and high ductility with excellent cold forging. Even if it is not subjected to spheroidizing annealing and softening prior to molding into fasteners such as screws and bolts or molded parts such as shafts, cracks are generated by severe molding such as recess molding. It is possible to manufacture fastening parts such as screws and bolts or molded articles such as shafts without any problems. Such material characteristics of the steel and the like according to the present invention exert a great effect such as omission of a manufacturing process of a fastening part such as a screw and a bolt or a molded product such as a shaft and reduction of manufacturing cost.

(8) [Warm rolling: 350-800 ° C, desirably 400-600 ° C]
Furthermore, by rolling in a temperature range of 350 to 800 ° C. as a production history, a fine-grained ferrite structure is obtained, and as a result, the tensile strength of the material is improved. In addition, the reduction in aperture is suppressed and maintained at a high level. In this warm rolling, when the rolling temperature is desirably adjusted within a low temperature range of 400 to 600 ° C., the refinement of ferrite grains is further promoted, and the tensile strength is further improved.

(9) [Average plastic strain ≧ 0.7]
When the above-mentioned warm rolling is adjusted so that the average composition strain remaining in the material is 0.7 or more calculated by the three-dimensional finite element method, the tensile strength of the material is improved and the drawing is secured. It is very effective to be done.

(10) [Multi-directional, multi-pass rolling]
In the warm rolling temperature range, steel and the like prepared by rolling the material so that the average plastic strain becomes 0.7 or more by multi-pass rolling in multiple directions are more desirable. The reason for this is that when performing a multi-pass rolling in multiple directions on the material, the required cumulative rolling reduction ratio (“total area reduction ratio R” in the present application (corresponding to the above equation (1)) is added. The inventors have found that an ultrafine ferrite grain structure can be obtained through a process similar to that in the case of warm large strain compression processing by one pass, and based on this knowledge, the required ultrafine grain is obtained. This is because it is possible to obtain a steel having a tensile strength with a diameter of ferrite as a main phase and a drawn steel, etc. Here, multi-pass rolling in multiple directions is described in claim 13 in the section of the solution means. This is the same as the rolling method as described in the description of the features of the invention.

[1-2] Fastened parts or shafts according to the invention of this application Molded parts such as screws and bolts according to the invention or shafts and other "molded products" Embodiments such as material characteristics will be described. The molded article according to the present invention has high strength, and is based on quantitatively defining both the form of the metal structure and the characteristics of the mechanical properties as described above. The material of the molded product is “wire or rod” included in “steel etc.” according to the present invention described in [1-1]. And it is manufactured by the processing method including forging using this as a raw material. This will be specifically described below.

(1) [Processing method including forging]
A “molded product” according to the present invention is manufactured by a processing method including forging a wire or bar excellent in strength and cold forgeability. The molded products according to the present invention are roughly classified into fastening parts such as screws and shafts such as shafts. Fastening parts include screws, bolts, nuts, rivets, stud bolts, fasteners, and other mechanical structural parts that have similar functions. On the other hand, shafts are used as shafts for transmitting rotational power. There are parts for mechanical structures consisting of various types of shafts. As a processing method including forging for manufacturing these molded products, among the above-mentioned molded products, a manufacturing apparatus conventionally used for manufacturing a desired type of fastening part is used for manufacturing a fastening part. The fastening component according to the present invention can be manufactured by an operation method suitable for the manufacturing apparatus. The typical processing methods include forging, rolling, cutting and forging, and these can be used in appropriate combination. On the other hand, for the manufacture of shafts, a forging device including a die suitable for manufacturing a desired type of fastening part and a cutting device can be used as appropriate for some processes. . Thus, the most important process in the process of processing the molded article according to the present invention is a process by forging in which material yield is high, the shape is high, the shape is complicated, and severe plastic processing is performed.

(2) [No tempering treatment required]
A molded product such as a fastening part or a shaft according to the present invention is molded by a processing method including forging using a wire or a bar included in the steel as a raw material. As described above, since the wire or bar according to the present invention has excellent strength, even after being formed and processed by a processing method including forging into a fastening part such as a screw and a bolt or a molded product such as a shaft. This strength characteristic is almost directly inherited by this molded product. Therefore, after being processed into a fastening part such as a screw and a bolt or a molded product such as a shaft, tempering treatment for the purpose of improving these mechanical properties, for example, improving strength, hardness, toughness, etc. Therefore, it is not necessary to perform any heat treatment such as quenching and tempering.

Furthermore, as described above, when manufacturing a small screw having a screw shaft diameter of 2.0 mm or less, such as an M1.6 pan head screw, residual stress after quenching or carburizing and quenching In some cases, heat treatment such as quenching may be difficult due to the relationship between the depth of the carburized layer and the screw diameter and thread size. is there. As described above, particularly when the screw has a shaft diameter of 1 mm or less, or is long, it may not be used as a machine part due to deformation accompanying quenching and tempering. In the manufacture of such a micro member, the supply of steel and the like according to the present invention is extremely effective. Thus, in the fastening parts such as screws and bolts or the molded products such as shafts according to the present invention, the fact that it is not necessary to perform the tempering treatment constitutes an extremely important part within the object of the present invention. It is a feature to do.
Of course, if it is necessary to further improve the mechanical properties for product-specific standards or special applications, etc., the tempering treatment can be performed as appropriate, and the molded product is subjected to the tempering treatment. Is not excluded from the molded product according to the present invention.

[2] Method for Producing Invention Group Next, a method for producing a steel having high strength and excellent cold forging according to the present invention (referred to as “the steel according to the present invention” in the present specification), and the present invention An embodiment of a method for producing a molded part such as a fastening part such as a screw and a bolt or a shaft excellent in strength according to the above will be described.

[2-1] Steel Manufacturing Method According to the Invention FIG. 4 shows the first half (up to the wire or bar 24) of the manufacturing process of the molded product such as a screw according to the invention. However, in the same figure, the wire or bar 24 refers to a material (material) having material properties suitable for molding in the next step as defined above. And this wire or bar 24 is included in the steel according to the present invention. Comparing the desirable process of the steel manufacturing method according to the present invention with the first half of the manufacturing process of the molded product such as a screw from the steel piece according to the prior art shown in FIG. 3 is manufactured by hot rolling or hot forging 2b to produce a steel wire or steel bar 4, and before supplying it to the processing steps including cold forming and rolling in the next step, spheroidizing annealing, etc. Heat treatment is an indispensable condition, but in the present invention, the semi-finished product 3 is manufactured by warm rolling 23 to produce a wire or bar 24, and the obtained wire or bar 24 is completely different. There is no need to perform heat treatment, and this can be supplied to processing steps including cold forging and rolling in the next step. This difference is because in the present invention, warm rolling 23 under appropriate conditions is performed instead of hot rolling or hot forging 2b as described above. Details will be described below.

The basics of the method for producing steel according to the present invention are as follows: 1) introduction of a predetermined area reduction rate, 2) The purpose is to perform caliber rolling by introducing a predetermined area reduction ratio by using a caliber roll, 3) introducing a predetermined plastic strain, or 4) defining a rolling condition parameter Z. Specifically, the essential requirement of the production method is that the warm rolling region is limited to a range of 350 to 800 ° C., and one of the following [Condition 1] to [Condition 4]. Meeting one or more. here,
[Condition 1] means that, in the introduction of a predetermined area reduction rate, from the immediately before the start of rolling represented by the above formula (1): R = {(S ₀ −S) / S ₀ } × 100 (%) to the end of rolling. Rolling so that the total area reduction R of the material is 50% or more,
[Condition 2] is that rolling is performed so that the total area reduction ratio R of the rolled material is 40% or more only when an oval hole mold is used for one pass or more.
[Condition 3] means adjusting the average plastic strain remaining in the material to 0.7 or more in the introduction of plastic strain, and
[Condition 4] is a plastic strain rate expressed by the above-mentioned formula (2): Z = log [(ε / t) exp {Q / (8.31 (T + 273))}] regarding the definition of the rolling condition parameter Z. The rolling is performed so that the value of the rolling condition parameter Z, which is a function of ε / t and the rolling temperature T, is 11 or more.

  In addition, in order to obtain a more desirable mode of the steel manufacturing method according to the present invention, it is appropriately specified that the rolling temperature range is narrowed, the heat treatment on the rolled steel may be restricted, and By defining other conditions, the manufacturing method of the invention group is configured. Details will be described below.

(1) Warm rolling temperature: about 350 to 800 ° C. When the rolling temperature is in the range of 350 to 800 ° C., a strain larger than a predetermined critical strain is introduced into the material, so that the crystal grains caused by this strain become microscopic. The difference in local orientation becomes the origin of fine crystal grains, and in the recovery process that occurs during or after processing, the dislocation density in the grains decreases and at the same time crystal grain boundaries are formed, so that a fine grain structure can be formed. That is, even when processing at a temperature of 800 ° C. or lower, which was regarded as the lower limit of the recrystallization temperature, dynamic recovery or recrystallization occurs at the same time as the processing, so that the crystal grains can be refined without using phase transformation. Can be achieved. However, if the processing temperature is too high, the crystal grains become coarse due to discontinuous recrystallization or normal grain growth. Thus, when the temperature exceeds 800 ° C., it is difficult to obtain fine crystal grains of 2 μm or less. On the other hand, if the processing temperature is too low, even if a strain larger than a predetermined critical strain is applied, recovery does not occur sufficiently, and a processed structure having a high dislocation density remains. Thus, when the rolling temperature is less than 350 ° C., it is difficult to obtain fine crystal grains of 2 μm or less. Therefore, in this invention, it is an essential requirement to limit the warm rolling temperature within the range of 350 to 800 ° C.

(2) [Condition 1]: Total area reduction ratio R ≧ 50%,
[Condition 2]: Only when an oval-shaped caliber roll is used, the total area reduction ratio R ≧ 40%, [Condition 3]: average plastic strain ε ≧ 0.7,
Or
[Condition 4]: Rolling condition parameter Z ≧ 11
About [Condition 1], [Condition 2] or [Condition 3], in the caliber rolling of steel slabs or steel materials with a C <0.45 mass% in the range of 350 to 800 ° C., the total area reduction rate When R is R ≧ 50%, or when using an oval caliber roll, R ≧ 40%, or when the average plastic strain ε of the steel piece or steel material is ε ≧ 0.7, The inventor found from the test results that subboundaries were introduced into the steel obtained after rolling, and the tensile strength TS was TS ≧ 600 MPa. At the same time, it was also found that an aperture of 65% or more (RA ≧ 65%) can be obtained. In addition, when the total area reduction ratio R or the average plastic strain ε is further increased, for example, when R ≧ about 83 to 95% or ε ≧ about 1.8 to 3.0, the large-angle grain boundaries occupy most of the tensile strength. The TS is further improved, and the aperture RA is also maintained or improved.

  In the above, the plastic strain introduced into the material in the actual operation of caliber rolling is generally unevenly distributed in the material. Here, the plastic strain obtained by averaging this nonuniform distribution, that is, the average plastic strain ε is used as an index. The average plastic strain amount can be expressed by an average plastic strain calculated by a three-dimensional finite element method. Further, as known as caliber rolls, there are three types of square type (square type or diamond type), round type and oval type. In this invention, there are two types of oval type, square type and round type. Broadly divided into The oval hole type caliber roll has a shape in which a hole formed by a combination of an upper mold and a lower mold has a flattened circular shape.

Regarding [Condition 4], in the caliber rolling of a steel slab or steel material with a C <0.45 mass% at a rolling temperature in the range of 350 to 800 ° C., the present inventors are Focusing on the fact that the average particle size of the ultrafine grains formed by large strain processing by pass) depends on the processing temperature and strain rate, Zener-Holomon parameter (= claim 2 according to claim 32). ) Formula): Z = log [(ε / t) exp {Q / (8.31 (T + 273))}] (where ε: average plastic strain, t: time from the start to the end of rolling (s), Q : Constant (254000 J / mol), T: rolling temperature (° C.), in the case of multi-pass rolling, a temperature obtained by averaging the rolling temperature of each pass), and the crystal grain size becomes finer as the rolling condition parameter Z increases. It was found that the reduction. The Zener-Holomon parameter was expressed in logarithmic form as shown in the above equation. FIG. 5 illustrates the relationship between the rolling condition parameter Z and the ferrite average grain size. That is, FIG. 5 shows that a fine grain structure having an average ferrite grain size of 1 μm or less can be obtained by controlling the rolling so that Z ≧ 11.
In the above rolling condition parameter Z, the average plastic strain ε can be calculated by a three-dimensional finite element method, but instead of this calculation method, the strain of the material (this can be obtained relatively easily in operation) It can be replaced to some extent by e) referred to in the specification as “industrial strain”. The industrial strain e is a function of the total area reduction ratio R, and is represented by e = −ln (1−R / 100).

Now, in addition to the essential requirements of the above items (1) and (2), by adding the conditions of the following items (3) to (6), a more desirable method for producing the steel according to the present invention is carried out. Can do.

(3) Multi-directional, multi-pass rolling Multi-directional multi-pass rolling is as described in the features of the invention according to claim 13, and the method involves appropriately rolling the rolled material in the longitudinal direction during caliber rolling. The rotation is performed around the axis within a range substantially less than 180 ° (not including 0 °). The reason why it is desirable to perform multi-directional and multi-pass rolling is as follows. In order to obtain a steel with an ultrafine grain structure by multipass rolling in multiple directions in the warm temperature range, 1) it is necessary to introduce a plastic strain larger than the required critical plastic strain into the material. From the viewpoint of ensuring the homogeneity of material properties after rolling, this plastic strain is desirably introduced as far as possible to 2) deep into the center of the material. This is because, when rolling with the same total area reduction ratio R is performed, the average plastic strain ε can be further increased by multi-directional, multi-pass rolling, and the plastic strain is further introduced deep into the material. Because it can be done.

  In addition, by using the oval-shaped caliber roll in [Condition 2], multi-directional multi-pass rolling is easily introduced and contributes to the increase in the average plastic strain ε. At the time of caliber roll rolling, the rolling direction is usually changed by rotating the material within a range of 0 ° to less than 90 ° for each rolling pass. At that time, when rolling with the square hole type next to the oval hole type, it is changed by 90 °, and when rolling with the oval hole type after the square hole type, it is changed by 45 °. In this way, the orientation of crystal grains can be dispersed to increase the number of fine grains surrounded by large-angle grain boundaries. It should be noted that even when two-pass rolling is performed continuously with the same caliber (so-called both cases), the material is rotated by 90 ° between the passes, which contributes to multi-directional multi-pass rolling.

  In the above, as the steel slab to be subjected to warm rolling, a steel ingot having a predetermined component is processed into a shape such as a bloom or billet by hot rolling or hot forging, and bloom or continuous casting or the like. Any of the slabs cast into a shape such as a billet may be used.

(4) About “2A ₀₁ / 2A ₀ ≦ 70/100” Now, the maximum minor axis length (denoted as 2A ₀₁ ) of the material after the above-described oval shape piercing rolling is defined as the opposite side length of the material before the rolling. It is 70% (2A ₀ and hereinafter) or less, i.e., 2A ₀₁ /
By controlling the amount of reduction so that 2A ₀ ≦ 70/100 (%), the amount of strain is largely controlled to contribute to the generation of fine grains. FIG. 6A shows the maximum minor axis length 2A ₀₁ of the material 19 after rolling by the oval shapes 18a and 18b, and FIG. 6B shows the opposite side length 2A of the material 20 before rolling. ₀ is schematically illustrated. Note that in FIG.
Reference numerals a (shaded portion) and 21b (shaded portion) show partial cross sections of the oval caliber. In this way, by performing rolling controlled so as to satisfy 2A ₀₁ / 2A ₀ ≦ 70/100 (%), it is possible to further apply a strain higher than the critical strain for generating fine grains to the deep part inside the material. It becomes easier, and it can be made more advantageous to make the ferrite grains have an average grain size of 1 μm or less over a wide range.

(5) More desirable rolling temperature control regulation rolling temperature: 400-600 ° C
Rolling stand-by or material cooling: (X + 1) Inlet material temperature at the first pass rolling: T _{X + 1, in} ≦ (T _X +30
) About ° C. Next, the temperature range in warm rolling is controlled within a more desirable range. As mentioned above, the microscopic local misorientation of the crystal grains caused by introducing large strains in the material by warm working becomes the origin of the fine grains, and in the recovery process that occurs during or after processing, intra-grain dislocations At the same time as the density decreases, a grain boundary is formed and a fine grain structure is formed. However, under complicated rolling conditions, the rolling temperature is low even in the range of the above-described warm rolling temperature of 350 to 800 ° C. If it is an eye, recovery may not be sufficient, and a processed structure having a high dislocation density remains. On the other hand, if the processing temperature is high, crystal grains may become coarse due to discontinuous recrystallization or normal grain growth, and it is difficult to obtain fine crystal grains of 2 μm or less. Therefore, in the present invention, in order to stably control the average particle size to 1 μm or less, it is desirable to control the rolling temperature within the range of 400 to 600 ° C.

On the other hand, processing heat is generated during rolling of the material. The amount of heat generated varies depending on the processing conditions. In order to obtain a fine grain structure with the desired grain size by controlling the temperature during rolling within a desired range, temperature control in consideration of the processing heat generation should be performed. Is desirable. Therefore, the material temperature at the rolling exit of a certain rolling pass (X pass) (for example, the material temperature within 1 second after rolling) T _{X, out}
However, when the temperature becomes higher by 30 ° C. or more than the rolling set temperature T _X, the material temperature T _{X + 1, in} at the rolling entrance of the next rolling pass (X + 1) pass is T _{X + 1, in} ≦ (T _X +30 ) Wait until it reaches ° C. or cool the material and continue rolling. However, the maximum temperature should not exceed 600 ° C. By doing so, the average grain size of the ferrite grains can be further refined, and can be aimed at 0.5 μm or less, for example. The temperature management method may be performed by a normal method according to the conventional technique. On the other hand, maintaining the lower limit 400 ° C. of the rolling set temperature is facilitated by processing heat generation, so if the material temperature just before the start of the first pass rolling is within the set temperature range, other than temperature behavior monitoring No special control is required.

(6) Spherical annealing treatment unnecessary Next, it is not necessary to perform spheroidizing annealing on the steel produced by the above-described steel production process according to the present invention. The reason for this is that, as described above, the steel according to the present invention is high in strength and has a high level of ductility of (65 to 70)% or more, so that it is required for the recess forming process of the screw head. It is because it is excellent in cold heading and does not generate defects such as recess cracks.

[2-2] Manufacturing Method of Fastened Parts such as Screws and Bolts or Molded Products such as Shafts According to the Invention Next, among the manufacturing methods of the invention product group of this application, the screws having excellent strength according to the invention An embodiment of a method for producing a fastening part such as a bolt or a molded product such as a shaft will be described.

(1) Basic process The basic process of the method of manufacturing a molded part such as a fastening part such as a screw and a bolt or a shaft according to the present invention is firstly described in the paragraph [1]. In addition, a method of producing a “steel excellent in cold forging” (method described in the above [2-1] section) is used to produce a wire or bar having high strength and excellent in cold forging. Then, by using this as a raw material, a processing method including forging is used to manufacture a fastening part such as a screw and bolt excellent in strength or a molded product such as a shaft. The form is as shown in FIG. That is, a steel slab or cast slab 22 having a predetermined component is processed into a semi-finished product 3 by hot rolling or hot forging 2a, and this is high strength by the warm rolling 23 described in the section [2-1] above. In addition, it is processed into a wire or bar 24 excellent in cold heading. This wire or bar 24 does not need to be subjected to any heat treatment 5 such as spheroidizing annealing as in the prior art shown in FIG. 6, a fastener 7 such as a screw and a bolt, or a molded product 7 such as a shaft is manufactured. The molded product 7 thus obtained does not need to be subjected to a tempering process 8 such as quenching and tempering in order to improve its mechanical properties to the required value as in the prior art shown in FIG. Then, the product is sent to the product line as it is, and is subjected to a surface treatment 9 such as plating as necessary to obtain a product 10. In the above, a conventional technique may be adopted as a processing method including forging. For example, in the manufacture of a screw, as described with reference to FIG. 12, the head portion of a screw material is formed by forging, a recess is formed by forging (header), and then a thread portion is formed by rolling. . Thus, the processing method including forging according to the prior art can be employed for the above-described wire or bar material having high strength and high ductility with excellent cold forging as described above. Because. It should be noted that in some of the screw manufacturing processes, a conventional cutting process may be employed as appropriate. Also, in the manufacture of other fastening parts such as bolts other than screws, conventional techniques may be used in accordance with the manufacture of the screws. On the other hand, shafts can also be manufactured in the same manner as fastening parts by a manufacturing process including forging by using an appropriate mold or the like.

(2) Substitutable process: Partial forging of rolling process and / or replacement by pressing process As described above, the manufacture of fasteners such as screws and bolts or molded products such as shafts according to the present invention is the above (1). This is done by the basic process of the term. In that case, in the manufacturing process of the wire rod or bar which is provided with the basic process of the same item (1) and is excellent in cold forging, the material is warm-rolled with a caliber. Therefore, the relationship between the shape and size of this material and the shape and size of fastening parts such as screws and bolts or shafts according to the present invention, or the production line of the steel slab or steel material and the wire or bar As a partial replacement of the warm rolling process, the forging process or the pressing process, and further, both of these processes may be used in combination as appropriate, due to restrictions on the process operation with the warm rolling line for manufacturing. The reason for this is the processing temperature within the rolling temperature range (350 to 800 ° C.) of the items [2-1] and (1), and the total area reduction ratio R in this caliber rolling process is the lower limit of the item (2). Value (= 50%) or more, or if the total area reduction ratio R is rolled at R ≧ 40% only when an oval-shaped caliber roll is used, the chemical composition, metal that the wire or rod should have This is because the structure and material characteristics can be obtained, so that a desired high strength wire rod or bar material excellent in cold heading can be obtained. In addition, depending on the installation conditions of the equipment, the manufacturing process may be more advantageous in terms of manufacturing cost.

(3) Manufacturing method that does not require tempering treatment In this invention, after being processed into a fastening part such as a screw and bolt or a molded product such as a shaft, tempering treatment by quenching and tempering is performed. There is no need to apply it at all. The reason for this is that the wire or bar that is the material of the fastening parts such as screws and bolts or shafts according to the present invention has the high strength already described above, that is, the tensile strength of 600 MPa or more or 800 MPa or more. Therefore, the strength after being molded into a molded product such as a fastening part or shaft is substantially inherited. That is, it can be used as a fastening part such as screws and bolts of various strength levels or a molded product such as shafts. In addition, as described above, when it is necessary to further improve the mechanical properties in accordance with the product-specific standards, the tempering treatment can be appropriately performed.

  Hereinafter, the present invention will be described in more detail with reference to examples.

[Test I: Examples 1 to 6, Comparative Example 1]
Test method Examples 1 to 6 were tested as follows. Ingredient No. shown in Table 1 Each steel having a chemical composition of 1 to 6 was melted using a vacuum melting furnace, cast into a steel ingot, and formed into an 80 mm square steel bar by hot forging. The metal structure of the obtained steel bar was composed of ferrite and pearlite. A rolled material was collected from the 80 mm square steel bar thus obtained, formed into a 18 mm square bar by multi-directional multi-pass caliber rolling in the warm, and then cooled with water to prepare a bar. The rolling method during this period is that the 80 mm square rolled material is heated to 550 ° C. and then rolled at a rolling temperature of 450 to 530 ° C. with a diamond-type caliber roll for 19 passes to form a 24 mm square (at this stage). The length corresponding to 2A ₀ in FIG. 6B is 24 mm),
Then, the maximum short axis length (length corresponding to 2A ₀₁ in FIG. 6A) is 11 mm and the long axis length (length 2c in FIG. 6A) is 52 mm. One-pass rolling was performed with a type caliber roll, and finally a 18 mm square bar was manufactured with a square type caliber roll.

As described above, in Examples 1 to 6, the total number of passes was 21 (= 19 + 1 + 1), and the total surface area reduction ratio (R according to the equation (1)) was 95%. The maximum minor axis length (2A ₀₁ = 11 mm) of the C-direction cross section of the material after rolling with the oval caliber roll is the opposite side length (2A) of the square C-direction cross section of the material immediately before rolling with the oval caliber roll. ₀ = 24m
m), (11/24) × 100 = 46%. In addition, during 19 passes by the diamond-type caliber roll, rolling (so-called through) that was performed in order to make the cross-sectional shape of the rolled material as close to a square as possible and passed through the same caliber roll for two consecutive passes was also counted. Yes. In addition, for each pass, the material was rotated around the longitudinal axis to change the rolling direction, and multi-directional multi-pass rolling was performed. In addition, due to the processing heat generation, the heat radiation amount is relatively small even in the rolling temperature region of the warm rolling, and there is no need for intermediate heating due to the temperature drop of the material during rolling.

  On the other hand, Comparative Example 1 was tested as follows. This is the result of performing caliber rolling at a high temperature outside the range of the present invention, and is as follows. Ingredient No. shown in Table 1 Using an 80 mm square steel bar obtained in the same manner as in Example 1 from the steel ingot of 1 and using the same caliber roll as in Examples 1 to 6 within the rolling temperature range of 880 to 920 ° C, It rolled by the method and the 18-mm square bar was manufactured from the 80-mm square steel bar. However, in order to ensure the rolling temperature during this period, intermediate heating was appropriately performed.

The following accuracy tests were performed on the bars of Examples 1 to 6 and Comparative Example 1 obtained as described above.
(1) Tensile strength TS and drawing RA were measured by a tensile test.
(2) The microstructure of the main phase (first phase), the average ferrite particle size measurement of the cross section in the C direction, the identification of the microstructure of the second phase and the fraction measurement of the second phase are performed by microstructural examination using a microscope. It was. In addition, the fraction (volume%) measurement of the 2nd phase measured the area% in a sample cross section, and evaluated this. And furthermore,
(3) For cold heading evaluation, a wire rod of 1.3 mmφ which is a material for forming a JIS standard M1.6 pan head screw from the above 18 mm square (however, only Comparative Example 2 is 63 mm square) is used. Similarly, a 1.3 mmφ test piece was cut and prepared by cutting, and a cross-shaped recess molding test was performed on the head by header molding for M1.6 pan head screws. The presence or absence of cracking at the time of recess molding is one of the decisive criteria for accepting or rejecting at the time of manufacturing the machine screw. Therefore, the presence or absence of recess cracks was observed with a 10 × magnifier. FIG. 7 and FIG. 8 exemplify external appearance photographs of those in which no recess cracks occurred and those in which they occurred.

  Table 2 shows main manufacturing conditions and test results of Examples 1 to 6 and Comparative Example 1 described above.

○ Test results From the above results, the following items can be understood.

[Examples 1 to 6] Examples 1 to 6 are in the low C region where the C content is 0.001 to 0.022% by mass, the rolling temperature range is 450 to 530 ° C, and the range of the warm rolling region. The opposite side length of the square-shaped material immediately before rolling, which is in a more desirable temperature range, and has a total area reduction ratio of 95%, which uses an oval type caliber roll, and which has a maximum short axis length. The ratio 2A ₀₁ / 2A ₀ to the height is 46%, which is quite small. Thus, the steel manufacturing method according to the present invention generally corresponds to extremely desirable conditions. The metal structure and mechanical properties of the steel obtained here are as follows.

  Regarding the metal structure, the main phase (first phase) is a ferrite structure having an average ferrite particle size of 0.7 to 0.9 μm, and the ferrite particle size of the main phase is remarkably refined. Therefore, the tensile strength TS is 635 to 795 MPa, satisfies the strength level required by the present invention, and the drawing RA, which is an important index of cold heading in this invention, is as high as 78% or more, and the lower limit target. The value 65% is fully satisfied.

  Thus, since the production conditions of the steels of Examples 1 to 6 belong to desirable conditions among the conditions within the scope of the present invention, extremely excellent characteristic values are obtained for both the metal structure and the mechanical properties. I understood.

  [Comparative Example 1] In contrast to Examples 1 to 6, Comparative Example 1 was a hot rolling region at 880 to 920 ° C, which is a region where the rolling temperature is outside the range of the present invention. In spite of the fact that the production conditions other than those described above were desirable, the obtained steel was not refined as an average ferrite grain size of 14.5 μm as its characteristic value, and therefore the tensile strength TS was 300 MPa. It was not satisfactory and was outside the scope of the present invention. In addition, since the drawing RA was as excellent as 80.0%, it was excellent in cold heading, and no recess crack was generated. However, in the steel of Comparative Example 1, a product formed into a screw or the like by cold heading or rolling cannot satisfy the lower limit 600 MPa of the target tensile strength of the present invention as it is.

[Test II: Examples 7 to 9, Comparative Examples 2 to 4]
Test method Examples 7 and 8 were tested as follows. Ingredient No. shown in Table 3 Steels having chemical composition compositions of 7 and 8 were melted using a vacuum melting furnace, cast into a steel ingot, and formed into a 115 mmφ round bar by hot forging. The metal structure of the obtained round bar was composed of ferrite and pearlite. Rolled materials were collected from the round bars having the respective chemical composition obtained as described above, formed into 18 mm square bars by warm multi-pass caliber rolling, and cooled by water to prepare bars. The rolling during this period consists of the following “first stage rolling” and “second stage rolling”. That is, after a rolled material of 115 mmφ was heated to 900 ° C., it was formed into 80 mm square by 10-pass rolling with a diamond-type caliber roll at a rolling temperature of 750 to 720 ° C. (so far, “first stage rolling” (= 10 Pass)). Next, this was air-cooled to 550 ° C., and then rolled at a rolling temperature of 550 to 500 ° C. with a diamond-type caliber roll for 19 passes to form a 24 mm square (at this stage, 2A in FIG. 6B). _The length corresponding to ₀ is 24 mm), and then the maximum short axis length (the length corresponding to 2A ₀₁ in FIG. 6A) is 11 mm and the long axis length (FIG. 6A). One pass rolling was performed with an oval type caliber roll having a length of 2 c in the middle of 52 mm, and then a 18 mm square bar was produced with a square type caliber roll (this was called “second stage rolling” (= 21 passes). )).

  As Example 9, the component Nos. Shown in Table 3 were used. A 115 mmφ round bar obtained from the steel ingot of No. 7 in the same manner as in Example 7 was heated to 500 ° C. and adjusted so that the rolling temperature was in the range of 480 to 450 ° C., and the same caliber roll as in Example 7 Was used to form a 18 mm square bar with the same pass schedule (= 31 passes) and cooled with water to prepare a bar. In particular, in Example 9, when the material temperature was higher by 30 ° C. or higher than 450 ° C. which is the set temperature after rolling a pass due to processing heat generation, after waiting until it became 480 ° C. or lower, the next The rolling pass was taken.

As described above, in each of Examples 7 to 9, the total number of passes is 31 (= 10 + 21), and in Examples 7 and 8, the substantial surface area reduction ratio of the material in the first stage is 40%. The total area reduction ratio (R according to the above equation (1)) of the materials of the first stage and the second stage was 98%. Also in Example 9, the total area reduction ratio R of the material was 98%. In any of Examples 7 to 9, an oval type caliber roll was used in the 30th pass, and the maximum minor axis length (2A ₀₁ = 11 mm) of the cross-section in the C direction of the material after the 30th pass rolling was With respect to the opposite side length (2A ₀ = 24 mm) of the square C direction cross section of the material immediately before rolling by this oval type caliber roll,
11/24) × 100 = 46%, which is a considerably small value. In addition, in order to make the cross-sectional shape of the diamond-type caliber roll rolled material as close to a square as possible, rolling (so-called so-called) that passes two consecutive passes through the same caliber roll was appropriately performed. In addition, for each pass, the material was rotated around the longitudinal axis to change the rolling direction, and multi-directional multi-pass rolling was performed.

  On the other hand, Comparative Examples 2 and 3 were tested as follows. This is because each component No. in Table 3 has a C content of 0.45% by mass which is outside the range of the present invention. 9 and 10 steel ingots were used. Among them, Comparative Example 3 had a high P content of 0.098% by mass. Except for these, the other conditions were the same as in Examples 7 and 8, pass schedule and rolling. Under the same conditions such as temperature, an 18 mm square bar was manufactured from a 115 mmφ round bar through the rolling of the “first stage” and the “second stage”.

  On the other hand, Comparative Example 4 has a chemical component composition of a raw material for manufacturing a standard product conventionally used as a relatively high-strength machine structural component. 11 (C: 0.30% by mass), 18 mm square steel bar with a total area reduction R = 60% by rolling 20 passes with a caliber roll within a rolling temperature range of 1100 to 800 ° C. It is molded into However, an oval-shaped caliber roll is not used in rolling. And if it is an original standard product, the spheroidizing annealing process should be performed and the ductility should be improved. However, in Comparative Example 4, the caliber rolling is still performed and the heat treatment is performed. Absent.

About the bar material of Examples 7-9 and Comparative Examples 2-4 obtained by the above, the same accuracy test as having been done by [Test I] was done in the same way.

  Table 4 shows main production conditions and test results of Examples 7 to 9 and Comparative Examples 2 to 4 described above.

○ Test results From the above results, the following items can be understood.

[Examples 7 to 9] Examples 7 to 9 are in the low to medium C region where the C content is 0.05 to 0.15 mass%, and the rolling temperature ranges are 750 to 700 in Examples 7 and 8. On the other hand, Example 9 is a test in which the temperature is controlled to a narrow and low temperature range of 480 to 450 ° C., which is a lower preferable temperature range. And all the area reduction ratios R are the cases of Examples 1 to 6 of Test I (R =
95%), which was 98%, and in the same manner as in Examples 1 to 6, the oval type caliber roll was used in the second pass from the last, and the square type caliber roll was used in the final pass. Here, the oval and square caliber rolls are the same as those used in Examples 1-6. Accordingly, 2A ₀₁ / 2A ₀ in the final two passes (30th and 31st passes) is 11 mm / 24 mm = 46%, which is considerably small as in the first to sixth embodiments.

  As described above, Examples 7 and 8 are generally highly desirable conditions among the steel manufacturing methods according to the present invention. And in Example 9, compared with Examples 7 and 8, the rolling temperature range is controlled to a narrow range in the low temperature range, and even compared to Examples 1 to 6, it is controlled to a narrower range in the low temperature range. In addition, the total area reduction ratio R is further increased (R = 95 → 98%). Therefore, it is as follows when the characteristic of the obtained steel is considered comparing with Examples 1-6.

  [Comparison between Examples 7 and 8 and Examples 1 to 6] When Examples 7 and 8 are compared with Examples 1 to 6, in Examples 7 and 8, 1) For the tensile strength TS, the total area reduction rate The point that R increased from 95 to 98% was effective, and the average ferrite grain size tended to be further reduced from 0.7 to 0.9 μm → 0.5 to 0.6 μm. Therefore, the tensile strength TS However, a strengthening increase effect is recognized from 635 to 795 MPa → 718 to 848 MPa. 2) Regarding the drawing RA, from 78.1 to 81.9% to 72.6 to 81.1%, reflecting the fact that the rolling temperature range was expanded to the high temperature side and the C content increased. A slight downward trend is observed.

  [Comparison of Example 9 and Examples 1-6] When Example 9 is compared with Examples 1-6, in Example 9, 1) For tensile strength TS, the total area reduction ratio R is 95 → 98%. And the point that the rolling temperature is in the range of Examples 1 to 6 and is further controlled in the low temperature region is effective, and the average ferrite grain size is 0.7 to 0.9 μm → 0.6 μm. Therefore, the tensile strength TS is significantly increased from 635 to 795 MPa to 884 MPa. 2) As for the aperture RA, a slight downward trend is observed from 78.1 to 81.9% → 74.7%, reflecting the increase in the C content.

[Comparison between Example 9 and Example 7] The chemical composition of both was the same, and 1) the average ferrite particle size was 0.6 μm in all cases, but in Example 9, the tensile strength TS was 718MPa → 884MPa, a significant strengthening increase effect is recognized. 2) Regarding the aperture RA, in Example 9, a clear decrease of 81.1% → 74.7% is recognized. This is considered to be because the rolling temperature of Example 9 was limited to a lower temperature region than Example 7. (The effect of rolling temperature on tensile strength TS and drawing RA will be further clarified in Test IV.)
As described above, with respect to the aperture RA, Example 9 is slightly lower than Examples 7 and 8, and Examples 7 and 8 are slightly lower than Examples 1 to 6. However, the aperture RA of Example 9 is still at a high level of 74.7%, sufficiently satisfies the target of 65% or more in the present invention, does not cause recess cracking, and is excellent in cold heading. It was confirmed that

[Comparative Examples 2 and 3] In Comparative Examples 2 and 3, since the C content was 0.45% by mass, which was outside the range of the present invention, other production conditions such as rolling temperature and total area reduction rate R were obtained. Examples 7 and 8
Like the above, it was within the scope of the present invention, but the second phase region was wide and exhibited a pearlite structure. Therefore, the diaphragm R is about 64 to 52% and does not satisfy the lower limit target value (65%) of the present invention. Therefore, recess cracks also occurred. Further, when comparing Comparative Example 2 and Comparative Example 3, the P content in Comparative Example 3 was as high as 0.098% by mass, so that the tensile strength TS was improved as compared with Comparative Example 2, but the aperture RA was It is inferior to Comparative Example 2.

  [Comparative Example 4] In Comparative Example 4, the C content is 0.30% by mass, which is slightly higher, but is within the scope of the present invention. However, since the rolling temperature is 1100 to 800 ° C. and the hot rolling region, the pearlite structure occupies the second phase, the second phase fraction is high, the drawing RA is inferior (38.0%), and the recess cracks. There has occurred.

[Test III: Examples 10 to 14]
Test Method In Test III, the influence of the total area reduction ratio of the material in the warm rolling on the material properties such as the metal structure and mechanical properties of the steel according to the present invention was tested.

  Examples 10-14 were tested as follows. Ingredient No. having chemical composition equivalent to steel standard SM490 shown in Table 5 12 steels were melted using a vacuum melting furnace, cast into a steel ingot, and formed into 80 mm square steel bars by hot forging. The metal structure of the obtained steel bar was composed of ferrite and pearlite. Roll material is collected from the steel bar obtained in this way, the rolling temperature is adjusted within the range of 450 to 520 ° C, it is formed into 5 size square bar steel by multi-directional multi-pass caliber rolling, and water-cooled to prepare the bar material did. The caliber rolls used were a square type and a diamond type, and were formed into bars by setting five levels of 51%, 79%, 91%, 95%, and 98% as the total area reduction R of the material (80 mm above) From the corners, they were formed into 56 mm square, 37 mm square, 24 mm square, 18 mm square and 12 mm square, respectively). The number of caliber rolling passes corresponding to each bar forming is 8 passes, 16 passes, 25 passes, 28 passes, and 32 passes. Table 6 shows these main production conditions.

About the bar material of Examples 10-14 obtained by the above, the accuracy test was done according to the test done by [Test I] and [Test II]. Table 6 also shows the test results.

○ Test results From the above results, the following items can be understood.

[About Examples 10 to 14] The characteristics of the manufacturing conditions between the tests of Examples 10 to 14 are that the number of rolling passes increases in order from Example 10 to Example 14, and the total area reduction rate R Is increasing. As the total area reduction ratio R increases from 51% to 98%, the tensile strength TS increases from 695 MPa to 904 MPa. On the other hand, the drawing RA, which is an index of cold heading, improves from 69.0% to 72.0% at first as the total area reduction ratio R increases, but starts to decrease immediately, and the total reduction When the surface area R is 98% (Example 14), the aperture RA is reduced to 68.7%. However, the level of the drawing RA value exceeds the target lower limit drawing RA value (65%) of the steel of the present invention, and excellent cold forgeability is maintained.

  Thus, within the scope of the present invention, it is confirmed that the tensile strength TS increases as the total area reduction ratio of the material increases, while the aperture RA shows a declining trend after showing the maximum value. all right.

[Test IV: Examples 15 to 17]
Test Method In Test IV, for the examples within the scope of the present invention, the influence of the rolling temperature level on the material properties such as the metal structure and mechanical properties of the steel according to the present invention was tested.

  Examples 15-17 were tested as follows. Ingredient No. having chemical composition equivalent to steel standard SM490 shown in Table 7 15 steel was melted using a vacuum melting furnace, cast into a steel ingot, and formed into a 24 mm square steel bar by hot forging. The metal structure of the obtained steel bar was composed of ferrite and pearlite. A rolling raw material is collected from the bar steel thus obtained, and the rolling temperature is adjusted within the respective ranges of 580 to 650 ° C., 480 to 550 ° C. and 380 to 450 ° C., and an 18 mm square bar is obtained by multi-directional multi-pass caliber rolling. Each bar was prepared by forming into a material and cooling with water. The used caliber roll was rolled in two passes, with the first pass being an oval type and the second pass being a square type. The average plastic strain ε of the material at this time was ε = 2.0 as a result of calculation by a three-dimensional finite element method. Table 8 shows main production conditions of Examples 15 to 17.

The bar material of each Example obtained as described above was subjected to a reliability test in accordance with the test performed in [Test III]. Table 8 shows the test results of Examples 15 to 17 described above.

○ Test results From the above results, the following items can be understood.

  [About Examples 15 to 17] The characteristic of the production conditions between Examples 15 to 17 is that the rolling temperature is lower from Example 15 to Example 17. As the rolling temperature is lowered from 580 to 650 ° C. → 480 to 550 ° C. → 380 to 450 ° C., the average ferrite grain size of the main phase becomes finer as 1.2 μm → 0.6 μm → 0.5 μm, so that tensile strength is increased. TS is correspondingly improved from 630 MPa → 833 MPa → 962 MPa. On the other hand, the drawing RA, which is an index of cold heading property, shows a downward trend of 78.1% → 73.1% → 72.0%.

  Thus, within the scope of the present invention, it was confirmed that the tensile strength TS increased as the rolling temperature decreased, while the drawing RA showed a decreasing tendency.

In addition, when the manufacturing conditions of Example 16 and Example 10 are compared, the total area reduction ratio R is the same at about 50%, the rolling temperatures are similar at 480 to 550 ° C. and 450 to 520 ° C., respectively, and the chemical composition is the same. C = 0.15 to 0.16% by mass and P = 0.0.10 to 0.011% by mass are almost the same, but only the pass schedule is greatly different. That is, in Example 16, rolling is performed from a 24 mm square material to an 18 mm square bar by two passes of an oval type → square type caliber roll. Here, the maximum minor axis length of the first-pass oval caliber roll (2A ₀₁ = 12 mm in FIG. 6) and the opposite side of the steel bar (C-direction cross-sectional shape size: 24 mm square) immediately before the first-pass rolling The ratio (2A ₀₁ / 2A ₀ ) to the length (2A ₀ = 24 mm in FIG. 6) is as small as 12 mm / 24 mm = 50%, that is, a large pressure strain due to one pass is introduced. Therefore, when the average plastic strain ε is calculated by calculating the plastic strain by the three-dimensional finite element method in this case, ε = 2.0. On the other hand, in Example 10, it is rolled from 80 mm square material to 56 mm square bar material by 8 passes using a square type and diamond type caliber roll. In this case, the average plastic strain ε can be obtained by the industrial plastic strain e according to the above-described equation (3), and e = 0.7 is obtained. As a result, Example 16 is superior in tensile strength TS (695 → 833 MPa), and Example 16 is slightly superior in terms of aperture RA (69.0 → 73.1%). As a cause of this, it is considered that the average plastic strain remaining in the material in Example 16 was larger due to the difference in the pass schedule (large reduction per pass and use of an oval type caliber roll). .

[Test V: Examples 18 and 19]
Test Method In Test V, a prototype experiment of a speed reduction shaft (Example 18) and a stepped pin (Example 19) was performed as shafts according to the present invention, targeting the examples within the scope of the present invention. As the material, the 18 mm square bar material obtained in Example 8 described in [Test II], which is steel according to the present invention, was used, and the test material was collected therefrom. From the 18 mm square bar material, a test piece having a predetermined size was cut out by cutting to simulate the respective materials for the reduction shaft (Example 18) and the stepped pin (Example 19). . This was cold forged and formed into a stepped pin with a diameter of 1.2 mmφ × total length of 18.5 mm and a head diameter of 2.5 mmφ × total length of 5 mm.

  9 and 10 show enlarged appearance photographs of the formed reduction shaft and stepped pin, respectively.

Test results No cracks were observed in any of Example 18 (deceleration shaft) and Example 19 (stepped pin), and a molded article with good surface properties was obtained. The dimensions and accuracy of the molded product are good, and the molding yield is substantially 100% in any of the examples. These are significant improvements of about 30 to 35% compared to the level of processing yield according to the prior art.

  As described above, the quality of the shafts according to the present invention is good, and it can be manufactured with high yield, energy saving and process saving, because the material characteristics have high strength with excellent cold heading. By being steel.

From the above tests I to V, it was confirmed that the steel having high strength and excellent cold forgeability according to the present invention was manufactured by the manufacturing methods of various aspects of the steel according to the present invention. Moreover, it turns out that molded articles, such as fastening parts, such as a screw and a volt | bolt excellent in the strength which concerns on this invention, or shafts, are manufactured using these steels.

M1 which requires severe cold forging in relation to the tensile strength TS and elongation El in a rolling test material with a high reduction in area by warming and multi-pass rolling in multiple directions in a Si-Mn based carbon steel material. FIG. 6 is a diagram illustrating the presence or absence of cracking during recess molding of a pan-head screw. Ferrite average grain diameter d and tensile strength TS in warm multi-directional multi-pass rolling test material (crystal structure: bcc) with large strain introduced for Si-Mn based carbon steel with various chemical composition changes It is a graph which illustrates the relationship with. M1 which requires severe cold forging in relation to the tensile strength TS and the drawing RA in a rolling test material with a high reduction in area due to warm and multi-pass rolling in multiple directions of a Si-Mn based carbon steel material. FIG. 6 is a diagram illustrating the presence or absence of cracking during recess molding of a pan-head screw. It is an example of the general | schematic flowchart of a manufacturing process until molded articles, such as fastening parts, such as a screw and a bolt, or shafts, from a steel piece etc. which concern on this invention. It is a graph which illustrates the relationship between the rolling condition parameter Z and a ferrite average particle diameter. Opposite sides of the oval shape of the grooved largest rolling the material after the short axis length 2A ₀₁ and pre-rolling of the material thereof is a schematic illustration of a length 2A _0. It is an example of the magnifier photograph of the parietal part which did not generate a recess crack at the time of manufacture of the small screw which concerns on the Example of this invention, and was sound. It is an example of the magnifier photograph of the top of the head although the recess crack occurred at the time of the machine screw manufacture which concerns on a comparative example. It is an example of the magnifier photograph which shows the external appearance of the deceleration shaft which concerns on the Example of this invention. It is an example of the magnifier photograph which shows the external appearance of the stepped pin which concerns on the Example of this invention. It is a general | schematic flowchart of the conventional manufacturing process until fasteners, such as a screw and a bolt, or molded articles, such as shafts, are manufactured from a steel piece. It is a conceptual diagram explaining the example of the header processing method in the case of shape | molding the head of a machine screw by cold heading.

Explanation of symbols

1 Steel slab 2a, 2b Hot rolling or hot forging 3 Semi-finished product 4 Steel wire or steel bar 5 Heat treatment 6 Cold forging and rolling 7 Fastening parts such as screws and bolts or moldings such as shafts 8 Conditioning treatment 9 Surface treatment 10 Product 11 Die 12a First punch 12b Second punch 13 Cut steel wire (material)
14 Head 15 Recess 16 Intermediate molded product 17 Intermediate molded product 18e, 18b formed with recess: Oval shape 19: Material after rolling by oval shape hole 20: Material 21a before rolling by oval shape hole shape, 21b: Partial cross section of oval-shaped caliber 22 Steel slab or slab 23 Warm rolling 24 Wire or bar 25 Cutting

Claims (28)

  Among the chemical composition, C: less than 0.45% by mass, having a ferrite structure as a main phase, having a mechanical property with a drawing of 65% or more and a tensile strength of 600 MPa or more, and quenching Or a steel having high strength and excellent cold forging, characterized by being not subjected to quenching or tempering treatment.   Among the chemical composition, C: less than 0.45% by mass, having a ferrite structure as a main phase, having a mechanical property with a drawing of 70% or more and a tensile strength of 800 MPa or more, and quenching The steel having high strength and excellent cold heading properties according to claim 1, wherein the steel is not subjected to quenching / tempering treatment.   The steel having high strength and excellent cold heading properties according to claim 1 or 2, wherein the ferrite structure has a main phase of a ferrite structure having an average grain size of 2 µm or less in a cross section perpendicular to the rolling direction. .   4. The steel having high strength and excellent cold forging properties according to claim 3, wherein the ferrite structure has a main phase of a ferrite structure having an average grain size of 1 μm or less in a cross section perpendicular to the rolling direction.   The steel having high strength and excellent cold heading properties according to any one of claims 1 to 4, wherein spheroidizing annealing is not performed. The steel has the following chemical composition:
C: Less than 0.45% by mass,
Si: 2.0 mass% or less,
Mn: 3.0% by mass or less,
P: 0 to 0.2% by mass or less,
S: 0.03 mass% or less,
The high-strength and cold-cooling according to any one of claims 1 to 5, wherein Al: 0.1% by mass or less, and N: 0.02% by mass or less, with the balance being Fe and inevitable impurities. Steel with excellent inter-forging properties.   The steel is characterized in that the second phase metal structure is mainly cementite, and the balance consists of one or more of pearlite, martensite, bainite, and a mixture of martensite and austenite. Item 6. The steel according to any one of items 1 to 6, having high strength and excellent cold forging.   The steel having a high strength and excellent cold heading property according to any one of claims 1 to 6, wherein the second phase metal structure is cementite.   The high strength and cold heading according to any one of claims 1 to 8, wherein the steel has a double phase or single phase structure in which the fraction of the second phase is 0 to 2% by volume or less. Steel with excellent properties.   The high strength and cold heading according to any one of claims 1 to 9, wherein the steel is manufactured by rolling a material within a range of 350 to 800 ° C. Steel with excellent properties. The steel having high strength and excellent cold heading according to claim 10, wherein the steel is manufactured by rolling a material within a range of 400 to 600 ° C. .   The steel has a residual plastic strain introduced into the material by the rolling of 0.7 or more as an average plastic strain in the material calculated by a three-dimensional finite element method. Steel with high strength of 10 or 11 and excellent cold workability.   The high-strength and low-temperature steel according to any one of claims 10 to 12, wherein the steel is obtained by introducing plastic strain into the material by multi-pass rolling in multiple directions with respect to the material. Steel with excellent inter-forging properties.   A molded article such as a fastening part such as a screw and a bolt excellent in strength or a shaft, which is a molded article of steel according to any one of claims 1 to 13.   15. A molded article such as a fastening part such as a screw and bolt or a shaft or the like excellent in strength according to claim 14, wherein the molded article is manufactured from a wire or bar by a processing method including forging.   A tempering treatment is not performed, and a molded part such as a fastening part such as a screw and a bolt or a shaft excellent in strength according to claim 14 or 15. C: A method of producing steel by warm caliber rolling with respect to a steel slab or steel material containing less than 0.45% by mass, wherein the rolling temperature is in the range of 350 to 800 ° C., and the steel slab in the rolling or The following formula (1) for steel:
R = {(S0−S) / S0} × 100 (1)
However, R: Total area reduction (%)
S0: C-direction cross-sectional area of a steel slab or steel just before the start of rolling S: Rolling when the total area reduction ratio R expressed by the C-direction cross-sectional area of steel obtained after the end of rolling is 50% or more A method for producing steel that is strong and excellent in cold heading. C: A method for producing steel by warm caliber rolling with respect to a steel slab or steel material containing less than 0.45% by mass, wherein the rolling temperature is in a range of 350 to 800 ° C., and an oval hole mold is used. Performing caliber rolling consisting of one pass or more and one pass or more using a square or round hole mold, and the following slab or steel material in the rolling:
R = {(S0−S) / S0} × 100 (1)
However, R: Total area reduction (%)
S0: C-direction cross-sectional area of steel slab or steel just before the start of rolling S: Rolling at a total area reduction ratio R expressed by the C-direction cross-sectional area of steel obtained after the end of rolling is 40% or more. A method for producing steel that is strong and excellent in cold heading.   The maximum short axis length in the C-direction section of the material after rolling using the oval hole mold is the opposite side length of the material in which the C-direction cross section immediately before rolling using the oval hole mold is square. The method for producing steel having high strength and excellent cold forging properties according to claim 18, characterized by being 70% or less. C: A method for producing steel by warm caliber rolling with respect to a steel slab or steel material containing less than 0.45% by mass, wherein the rolling temperature is in the range of 350 to 800 ° C., and into the material by the caliber rolling. High strength, characterized by rolling the steel slab or steel material so that the plastic strain to be introduced and left is 0.7 or more in terms of the average plastic strain into the material calculated by the three-dimensional finite element method And the manufacturing method of steel excellent in cold forgeability. C: A method for producing steel by warm caliber rolling with respect to a steel piece or steel material containing less than 0.45% by mass, wherein the rolling temperature is in the range of 350 to 800 ° C., and the following formula (2):
Z = log [(ε / t) exp {Q / (8.31 (T + 273))}]
(2)
Where ε: average plastic strain t: time from the start to the end of rolling (s)
Q: Constant (254000 J / mol)
T: Rolling temperature (° C.) (Temperature of rolling temperature of each pass)
A steel manufacturing method having high strength and excellent cold heading, wherein rolling is performed so that a rolling condition parameter Z represented by   The method for producing steel with high strength and excellent cold heading properties according to any one of claims 17 to 21, wherein the caliber rolling in the warm is performed in multiple passes in multiple directions.   23. The production of steel having high strength and excellent cold heading properties according to any one of claims 17 to 22, wherein a rolling temperature of the steel slab or steel material is in a range of 400 to 600 ° C. Method. Regarding the rolling temperature of the steel slab or steel material, the set temperature is in the range of 400 to 600 ° C., and the material temperature TX, out at the rolling exit of the X pass (where X is a natural number) is the X pass When the temperature is higher by 30 ° C. than the preset rolling temperature TX, the material temperature TX + 1, in at the rolling entrance of the (X + 1) th pass, which is the next rolling pass, is TX + 1, in ≦ (TX + 30). ℃
24. The method for producing steel with high strength and excellent cold forging properties according to claim 23, wherein the rolling is continued after waiting until the temperature reaches or the material is cooled.   The high strength and cold heading property according to any one of claims 17 to 24, wherein after the rolling in the warm, the steel obtained by the rolling is not subjected to spheroidizing annealing treatment. Excellent steel manufacturing method.   A wire rod or bar manufactured by the method according to any one of claims 17 to 25 is subjected to processing including forging and formed, such as a fastening part such as a screw and a bolt excellent in strength or a shaft Manufacturing method of molded products.   In the manufacturing method of the fastening parts such as screws and bolts excellent in the strength or the molded products such as shafts, forging method and press work instead of the rolling method of at least a part of the steps included in the whole manufacturing process. The method of manufacturing a molded part such as a fastening part such as a screw and a bolt excellent in strength or a shaft according to claim 26, wherein at least one of the methods is used. In the manufacturing process of the fastening parts such as screws and bolts having excellent strength or the molded parts such as shafts, the molded article after being molded into the molded article is not subjected to tempering treatment. A method for producing a molded part such as a fastening part such as a screw and a bolt or a shaft having excellent strength according to claim 26 or 27.