JP2010202920A - Wire rod for high-strength steel wire, high-strength steel wire, and method for manufacturing them - Google Patents

Abstract

<P>PROBLEM TO BE SOLVED: To provide a steel wire which can be manufactured without being subjected to patenting treatment in a wire-drawing process, and has superior mechanical properties such as strength and tensile strength; a wire rod to be used for manufacturing the steel wire; and a method for manufacturing them. <P>SOLUTION: The hot-rolled wire rod is made from a steel containing 0.30-0.50% C, 0.1-0.4% Si, 0.2-1.0% Mn, 0.01% or less Al, 0.01% or less Ti, 4-30 ppm B, 15-35 ppm N and 15-35 ppm O; includes pro-eutectoid ferrite and bainite of which the area rate FA(%) is in a range satisfying FA≤-35×(%C)+22, and pearlite which occupies 95% or more of the balance; and has a wire diameter of 3.6-7 mm. The steel wire is obtained by wire-drawing the wire rod at a true strain of 4 or more without subjecting the wire rod to the patenting treatment and bluing treatment, has a wire diameter D of 0.2-0.4 mm, has such a TS (MPa) as to satisfy 3,950-D×2,600≤TS, and does not cause the occurrence of the delamination in a twist test. <P>COPYRIGHT: (C)2010,JPO&INPIT

Description

  The present invention relates to a technique for manufacturing an ultrafine steel wire excellent in strength, toughness, ductility, and the like without performing patenting treatment and bluing treatment during drawing.

  In order to manufacture steel wires for steel cords, which are typical examples of high-strength steel wires, usually high-carbon steel having a carbon content of about 0.7 to 0.8% [equivalent to JISG 3502 (SWRS72A, SWRS82A)] Use it, hot-roll it, and then control the cooling conditions to make a steel wire with a diameter of about 5.0 to 6.4 mm, then primary wire drawing, patenting treatment, secondary wire drawing, After a patenting treatment, Cu—Zn two-phase plating, and a diffusion treatment, it is manufactured to have a predetermined wire diameter by finally performing wet wire drawing (finish wire drawing).

  At this time, the patenting process is performed in order to obtain a uniform fine pearlite structure suitable for wire drawing. However, since the wire drawing limit in high carbon steel is usually as low as 4 or less at the true strain, the final wire drawing is performed. As the diameter becomes thinner, the wire diameter after the final patenting also becomes thinner, so that there is a problem that the number of patenting needs to be increased.

  Therefore, various improvement methods have been proposed for the purpose of improving the wire drawing limit and improving the wire drawing workability of the wire.

For example, Patent Document 1 discloses a method for suppressing precipitation of pro-eutectoid cementite that adversely affects wire drawing by controlling a cooling rate during patenting, and Patent Document 2 discloses a cross section of a hot-rolled wire rod. A technique for controlling the coarse pearlite rate in the tissue is disclosed.
Patent Documents 3 and 4 disclose a technique for improving the wire drawing limit by suppressing the increase in strength due to wire drawing by making the steel wire structure a bainite structure with little work hardening.
Patent Document 5 discloses that a medium carbon steel wire having a carbon content of 0.30 to 0.60% is used to control the tensile strength after final patenting, the pearlite structure, and proeutectoid ferrite, thereby limiting the wire drawing. A technique for improving the above is disclosed.

  According to these methods, it is possible to improve the wire drawing workability even if the number of patenting is less than the conventional method, but in any method, it is necessary to perform at least one patenting process during the wire drawing. is there.

  On the other hand, Patent Document 6 discloses a method capable of industrially producing an ultrafine wire having a wire diameter of 0.15 mm or less. Specifically, heat treatment is applied to a low carbon steel wire (C: 0.01 to 0.30%) to adjust to a mixed structure of ferrite and acicular martensite or bainite, and then the wire is processed mainly by wire drawing. Although a method for obtaining strength is disclosed, since the heat treatment strength is as low as about 70 kgf / mm 2 and the work hardening rate is also lower than that of pearlite steel, the heat treatment wire is applied when applied to an ultrafine wire of about 0.2 mm. The specified strength cannot be obtained unless the diameter is considerably increased and the wire drawing strain is increased, and in a large diameter heat treatment of 5.5 mm or more, the structure between the steel wire surface layer and the central portion tends to be non-uniform. There is a problem in that the formation of bulky martensite leads to early drawing breakage and deterioration of mechanical properties.

  Patent Document 7 describes a method of cooling after hot rolling of a medium and high carbon steel wire (C: 0.35 to 0.9%), adjusting to a structure containing pro-eutectoid ferrite with an area ratio of 20% or less, and Although a method of obtaining a high strength steel wire having a wire diameter of 0.15 to 0.4 mm by wire drawing without drawing is usually disclosed, in order to produce a steel cord filament, To ensure lubricity and adhesion to rubber, it is necessary to perform Cu-Zn two-phase plating and heat diffusion treatment (diffusion brass plating) during the wire drawing process. During the heat diffusion treatment of this plating (hereinafter, this treatment is referred to as bluing treatment), the stretched lamella structure formed by drawing is divided, so that the C amount of about 0.3 to 0.4% However, it was difficult to obtain a predetermined strength after wire drawing, and the ductility deteriorated.

  Furthermore, Patent Document 8 discloses a method of obtaining a steel wire by drawing a pearlite wire rod with discontinuous cementite without heat treatment. However, discontinuous cementite has a slow cooling rate. This is a structure that is inevitably obtained because of patenting equivalent to stealmore, and has a problem that strength is low because cementite is discontinuous.

Japanese Patent Laid-Open No. 5-98349 Japanese Patent Publication No. 3-60900 JP-A-5-105965 Japanese Patent Laid-Open No. 5-117744 Japanese Patent Laid-Open No. 6-2039 Japanese Patent Publication No. 1-15563 Japanese Patent No. 3499341 Japanese Patent No. 3409005

  Therefore, in view of the circumstances as described above, the present invention uses medium carbon steel as a raw material, and can be drawn into an ultrafine steel wire without any heat treatment such as patenting treatment and bluing treatment during the drawing step. In addition, it is possible to provide a high-strength, ultra-fine steel wire that can be obtained from an ultra-fine steel wire that does not cause delamination (longitudinal cracking) at the time of stranded wire. It is a problem to make.

  The inventors of the present invention use a medium carbon region steel material having a carbon concentration of 0.5% or less, first rolling, cooling, and patenting under various conditions to create a wire material having various structures and strength levels, and the wire material. Was used to draw an ultrafine steel wire having a diameter of 0.2 to 0.4 mm. And, mechanical properties such as tensile strength and torsional properties of these steel wires were investigated. And the steel material component which improves the mechanical characteristic of a steel wire, the rolling condition, the patenting condition, the influence of the wire drawing condition, etc. were examined repeatedly.

  As a result, while reducing the area ratio of proeutectoid ferrite + bainite structure which is a soft phase and using a rolled wire whose tensile strength is appropriately controlled according to the amount of C in the wire, intermediate patenting treatment and It is possible to produce ultra-fine steel wires without any heat treatment such as bluing treatment, and by applying such a wire to a final true strain of 4 or more, the final wire diameter can be reduced. The conclusion was reached that the steel wire with higher strength and no delamination can be obtained.

The present invention has been made on the basis of the above findings, and the gist thereof is as follows.
(1) By mass%, C: 0.30 to 0.50%, Si: 0.10 to 0.40%, Mn: 0.20 to 1.0%, B: 4 to 30 ppm, N: 15 Contains 35 ppm, O: 15-35 ppm, Al: 0.01% or less (including 0%), Ti: 0.01% or less (including 0%), and consists of the balance iron and unavoidable impurities, patenting Later tensile strength TS (MPa) is in the range of the following formula 1,
1000 × (% C) + 350 ≦ TS ≦ 1000 × (% C) +500
... (Formula 1)
And the area ratio FA (%) of pro-eutectoid ferrite and bainite is in the range of the following formula 2,
FA ≦ −35 × (% C) +22 (Formula 2)
95% or more of the balance is a pearlite structure, and the average block particle size of the pearlite structure is 20 μm or less, a high-strength ultrafine steel wire rod having a wire diameter of 3.6 to 7 mm.
(2) Further, in mass%, Cr: 0.5% or less, Ni: 0.5% or less, Co: 0.5% or less, Cu: 0.2% or less, Mo: 0.2% or less, W The wire for high-strength ultrafine steel wire according to (1) above, which contains at least one selected from the group consisting of 0.2% or less.

(3) A steel wire having a diameter D (mm) of 0.2 to 0.4 mm by drawing the wire according to (1) or (2) without performing heat treatment, A high-strength ultrafine steel wire that does not generate delamination and has a tensile strength TS (MPa) of 3000 MPa or more and satisfies the following formula 3.
3950−D × 2600 ≦ TS (Formula 3)

(4) The steel slab of the steel component described in (1) or (2) is hot-rolled, the finish rolling temperature is 1000 to 1200 ° C, and then wound at a temperature of 880 to 960 ° C, and then 520 to The method for producing a high-strength steel wire according to (1) or (2), wherein a patenting treatment including a step of immersing in a molten salt at a temperature of 580 ° C. for 30 s or more is performed.
(5) The steel slab of the steel component described in (1) or (2) is hot-rolled, the finish rolling temperature is 1000 to 1200 ° C, and then wound at a temperature of 880 to 960 ° C, and then 800 ° C. (1) or (2), characterized in that a cooling rate from 1 to 600 ° C. is set to 50 to 200 ° C./s, and thereafter a patenting process including a step of holding for 30 seconds or more in a temperature range of 520 to 580 ° C. is performed. The manufacturing method of the wire material for high-strength steel wires as described in).

  (6) The diameter D (mm) is in the range of 0.2 to 0.4 mm under the condition of true strain of 4% or more without subjecting the wire manufactured by the method according to claim 4 or 5 to heat treatment. The method for producing a high-strength ultrafine steel wire according to (3), wherein wire-drawing is performed until

  It is possible to obtain a wire that can be drawn into an ultrafine steel wire without performing any heat treatment such as patenting and bluing during the wire drawing process, and using the wire, high strength and twisted wire can be obtained. It is possible to obtain an ultra fine steel wire free from delamination (longitudinal cracking).

It is a figure which shows the relationship between the area ratio of the pro-eutectoid ferrite + bainite structure of a wire rod, and the tensile strength TS after wire drawing. It is a figure which shows the relationship between the wire diameter of the steel wire after wire drawing, and tensile strength. It is a figure which shows the relationship between C content of the used steel, and the tensile strength of a rolled wire. It is a figure which shows the relationship between C content of used steel, and the area ratio of pro-eutectoid ferrite + bainite structure. It is the figure using the SEM observation photograph which shows the typical pearlite structure | tissue of the steel wire which concerns on this invention.

  Usually, in order to obtain a steel wire for steel cord, after austenizing a wire having a carbon concentration close to that of eutectoid steel and containing about 0.2% of Si, it is several to several tens at 450 to 600 ° C. After performing a patenting process for holding for 2 seconds to obtain an almost complete pearlite structure, wire drawing is performed. However, in this method, since the wire strength before wire drawing is high and the work hardening coefficient at the time of wire drawing is large, breakage during wire drawing or delamination after wire drawing occurs with a true strain of about 3 to 4.

  Therefore, the present inventors first performed rolling, cooling, patenting, primary wire drawing, bonder coating treatment, and finish wire drawing under various conditions using steel materials in the medium carbon region with a carbon concentration of 0.5% or less. Steel wires with various strength levels having a diameter of 0.2 to 0.4 mm were prepared, and the tensile strength and steel structure of these steel wires were investigated. As a result, the following knowledge was obtained.

  (A) Using a steel material with the carbon content in the steel reduced to about 0.3 to 0.5%, suppressing the pro-eutectoid ferrite even if a patenting treatment is performed by a normal rolling / steelmore treatment. It is difficult and the tensile strength (TS) of the wire becomes low. Even if such a wire is drawn without patenting, it is difficult to obtain a high-strength wire having a predetermined TS with a true strain of 4 or more.

  (B) The steel material whose carbon content in the steel is reduced to about 0.3 to 0.5% is subjected to normal rolling to increase the cooling speed of the wire to about 500 ° C. Thus, pro-eutectoid ferrite can be suppressed, but by rapidly cooling to less than 520 ° C., bainite which is a supercooled structure is generated, and strength and ductility deteriorate. Even if such a wire is drawn, it is difficult to obtain a high-strength wire of a predetermined TS by drawing with a true strain of 4 or more.

  (C) When rolling into a wire using a steel material whose carbon content in steel is reduced to about 0.3 to 0.5%, the finish rolling temperature is 1000 to 1200 ° C, and then 880 ° C to 960 ° C. After rolling up at a temperature, the rolled γ grain size is coarsened by dipping in a molten salt at 520 to 580 ° C., and both pro-eutectoid ferrite and bainite are suppressed, and the remaining 95% or more is a pearlite structure. In addition, the pearlite block particle size usually exceeding 20 μm can be made 20 μm or less. By applying a wire having a true strain of 4 or more to such a wire, it is possible to obtain a steel wire having high strength and no delamination.

  Therefore, using a steel with a carbon content of 0.3 to 0.5% in steel, the rolling condition and the cooling condition after winding were changed, and a rolled wire rod with various amounts of proeutectoid ferrite and bainite was prepared. Furthermore, a steel wire having a wire diameter of 0.2 to 0.4 mm was created by subjecting the wire to wire drawing with a true strain of 4 or more without patenting and bluing.

The obtained rolled wire was examined for wire structure and tensile strength. In addition, the tensile strength of the steel wire after wire drawing was examined, and a twist test was conducted to examine whether delamination occurred.
First, the conditions for obtaining a high-strength steel wire were examined.

  Fig. 1 shows the relationship between the area ratio (fraction) of the proeutectoid ferrite + bainite structure of the wire rod and the tensile strength TS after wire drawing, and Fig. 2 shows the relationship between the wire diameter of the steel wire after wire drawing and TS. Indicates. In these figures, the open mark in the comparative example indicates that delamination has occurred.

  From FIG. 1, by reducing the area ratio of the pro-eutectoid ferrite + bainite structure of the rolled wire to 11, 5% or less, it is possible to produce a steel wire having a tensile strength of 3000 MPa or more and no delamination. I know that there is.

Further, from FIG. 2, if the relationship between the tensile strength TS (MPa) of the steel wire and the wire diameter D is in a range satisfying the following formula, a steel wire having high strength and no delamination can be obtained. You can see that it is possible.
3950-D × 2600 ≦ TS

  Here, the area ratio of the pro-eutectoid ferrite + bainite structure was determined by corroding the wire material with wet picric acid, then corroding with saturated picric acid for several seconds, and using an optical microscope at a magnification of × 500, the surface layer, 1 / 4D, 1 / 2D, Five images were taken, and the area fraction of proeutectoid ferrite + bainite structure (which looks white) was image-analyzed, and the average value thereof was obtained.

  Next, the conditions of the tensile strength of the rolled wire rod and the area ratio of pro-eutectoid ferrite + bainite structure to obtain a steel wire having high strength and no delamination when twisted were examined.

  FIG. 3 shows the relationship between the C content of steel and the tensile strength, and FIG. 4 shows the C content of steel, with respect to the rolled wire rod in which the steel wire shown in FIG. 1 has a TS of 2950 MPa or more and no delamination occurs. The relationship between the amount and the area ratio of proeutectoid ferrite + bainite structure is shown.

From FIG. 3, if the tensile strength TS (MPa) of the rolled wire material satisfies the relationship of the following formula according to the C content% C (mass%), a steel wire having high strength and no occurrence of delamination can be obtained. It turns out that it is obtained.
1000 × (% C) + 350 ≦ TS ≦ 1000 × (% C) +500

Further, from FIG. 4, if the area ratio FA (%) of the pro-eutectoid ferrite + bainite structure satisfies the relationship of the following formula according to the C content% C (mass%), a similar steel wire is obtained. I understand that
FA ≦ −35 × (% C) +22

The present invention was made by further optimizing the chemical composition of steel based on the above examination results, and the present invention will be further described below.
In the following description,% and ppm of the component content mean mass% and mass ppm, respectively.
First, the reasons for limiting the components of the steel wire used in the present invention will be described.

C: 0.30 to 0.50%
C is an effective and economical element for increasing the strength, and the amount of work hardening at the time of wire drawing and the strength after wire drawing increase as the C content increases. Furthermore, if the amount of C is small, it is difficult to reduce the amount of proeutectoid ferrite in the rolled wire rod. Therefore, in the present invention, the lower limit is required to be 0.3%. On the other hand, if the amount of C is too large, the strength of the wire becomes too high and the toughness and ductility of the steel wire during or after wire drawing is deteriorated, so the upper limit of the amount of C is made 0.50%. A preferable upper limit is 0.45%, more preferably 0.40%.

Si: 0.10 to 0.40%
Si is an element useful as a deoxidizer. If the content is less than 0.10%, the effect becomes insufficient, so the content is made 0.10% or more. On the other hand, since Si is a ferrite-forming element and has a function of degrading scale peelability, the upper limit was made 0.40%.

Mn: 0.20 to 1.00%
Mn, like Si, is an element useful as a deoxidizing agent, and 0.20% or more is necessary to make its effect sufficient. On the other hand, Mn has the effect of increasing the hardenability of the steel and reducing the amount of proeutectoid ferrite in the rolled material. Further, since it is also an element that is easily segregated, if it is added excessively, a supercooled structure such as martensite or bainite may be generated in the segregated portion of Mn and the wire drawing workability may be deteriorated. Therefore, the upper limit of the amount of Mn is set to 1.00%. A preferable upper limit is 0.80%.

B: 4 to 30 ppm
When B exists in the austenite in a solid solution state, it has an effect of concentrating at the grain boundary and suppressing precipitation of proeutectoid ferrite. Since B forms a nitride, it is necessary to consider the balance with the N amount in order to secure the B amount in a solid solution state. On the other hand, when B is added too much, coarse Fe ₃ (CB) ₆ carbide is generated in austenite, and there is a possibility that the wire drawing property is lowered. About these relations, the present inventors repeated experiment and set it as 4-30 mass ppm as the optimal range of B content. Preferably it is 6-20 ppm, More preferably, it is 8-12 ppm.

N: 15-35 ppm
N produces Al, B and nitride in the steel and has an effect of preventing coarsening of the austenite grain size at the time of heating, and the effect is effectively exhibited by containing 15 ppm or more. However, if the content becomes too large, the amount of nitride increases too much, and the amount of dissolved B in austenite is reduced. Further, solute N may promote aging during wire drawing. Therefore, the N content is within the range of 15 to 35 ppm.

O: 15-35 ppm
O forms complex inclusions that do not adversely affect the wire drawing characteristics by forming complex inclusions with Si and others. Such a soft inclusion can be finely dispersed after rolling, and has an effect of suppressing the excessive coarsening of the γ grain size by the pinning effect and improving the ductility of the patenting wire. Therefore, the lower limit is set to a value greater than 15 ppm. However, if the content is too large, hard inclusions are formed and the wire drawing characteristics deteriorate, so the upper limit of O was set to 35 ppm.

Al: 0.01% or less The Al content is 0.01% or less, including 0%, so that hard non-deformable alumina-based nonmetallic inclusions are generated and the steel wire is not ductile and drawn. Stipulated.

Ti: 0.01% or less The content of Ti is specified to be 0.01% or less including 0% so that a hard non-deformable oxide is generated and the steel wire is not ductile and drawn.

  The impurities P and S are not particularly defined, but are each preferably 0.02% or less from the viewpoint of ensuring ductility as in the case of conventional ultra fine steel wires.

The steel wire used in the present invention has the above-mentioned elements as basic components, but for the purpose of further improving mechanical properties such as strength, toughness, ductility, etc. Two or more kinds may be positively contained.
Cr: 0.5% or less, Ni: 0.5% or less, Co: 0.5% or less, Cu: 0.2% or less, Mo: 0.2% or less, W: 0.2% or less.
Hereinafter, each element will be described.

Cr: 0.5% or less Cr is an element effective for reducing the lamella spacing of pearlite and improving the strength of the wire and the wire drawing workability. Addition of 0.1% or more is preferable for effectively exhibiting such an action. On the other hand, if the amount of Cr is too large, the transformation end time becomes long, and there is a possibility that a supercooled structure such as martensite or bainite is generated in the hot-rolled wire, and the mechanical scaling property is also deteriorated. 0.5%.

Ni: 0.5% or less Ni does not contribute much to the strength increase of the wire, but is an element that increases the toughness of the wire. Addition of 0.1% or more is preferable for effectively exhibiting such action. On the other hand, if Ni is added excessively, the transformation end time becomes longer, so the upper limit was made 0.5%.

Co: 1% or less Co is an element effective for suppressing precipitation of pro-eutectoid cementite in the rolled material. Addition of 0.1% or more is preferable for effectively exhibiting such an action. On the other hand, even if Co is added excessively, the effect is saturated and economically useless, so the upper limit was set to 0.5%.

Cu: 0.2% or less Cu has an effect of increasing the corrosion resistance of the ultrafine steel wire. Addition of 0.1% or more is preferable for effectively exhibiting such an action. However, if added excessively, it reacts with S and segregates CuS in the grain boundaries, so that flaws are generated in the steel ingot, wire, etc. during the wire manufacturing process. In order to prevent such adverse effects, the upper limit was made 0.2%.

Mo: 0.2% or less Mo has an effect of increasing the corrosion resistance of the ultrafine steel wire. Addition of 0.1% or more is preferable for effectively exhibiting such an action. On the other hand, if Mo is added excessively, the transformation end time becomes long, so the upper limit was made 0.2%.

W: 0.2% or less W has an effect of enhancing the corrosion resistance of the ultrafine steel wire. Addition of 0.1% or more is preferable for effectively exhibiting such an action. On the other hand, if W is added excessively, the transformation end time becomes longer, so the upper limit was made 0.2%.

Next, the structure, strength, and manufacturing conditions of the rolled wire will be described.
A steel billet (steel piece) composed of the above components is heated and then hot rolled to obtain a rolled wire having a wire diameter corresponding to the final product diameter. In this invention, in order to obtain the ultra fine steel wire in the range of 0.2 to 0.4 mm, the wire diameter of the rolled wire is set to 3.6 to 7 mm.

At that time, by controlling the hot rolling conditions and the cooling conditions after hot rolling, the tensile strength TS (MPa) of the rolled wire after patenting is in the range of the following formula 1,
1000 × (% C) + 350 ≦ TS ≦ 1000 × (% C) +500 (Formula 1)
And the total area ratio FA of proeutectoid ferrite and bainite is in the range of the following formula 2,
FA ≦ −35 × (% C) +22 (Formula 2)
The remaining 95% or more is a pearlite structure, and the average block particle size of the pearlite structure is 20 μm or less.

  The tensile strength TS of the rolled wire is defined as described above in accordance with the C content. As shown in FIG. 3 above, if the relationship of Formula 1 is satisfied, delamination occurs with high strength. This is to make it possible to obtain a steel wire without any wire.

  Moreover, the area ratio of pro-eutectoid ferrite and bainite of the rolled wire is defined as described above, as shown in FIG. 4 above, with high strength and delamination without performing patenting treatment again during wire drawing. This is to make it possible to obtain a steel wire that does not generate any of the above. The total area ratio of pro-eutectoid ferrite and bainite may be 0%, but it is difficult to avoid their generation under normal manufacturing conditions.

  The reason why the area ratio of the pearlite structure is 95% or more of the remaining structure is that if it is less than 95%, the strength of the necessary wire cannot be secured and the ductility at the time of drawing decreases. The balance may be 100% pearlite structure.

  The reason why the average block particle size of the pearlite structure is limited to 20 μm or less is to ensure the ductility of the wire. Usually, the pearlite block particle size increases with the coarsening of the γ particle size, but as described below, by immersing in molten salt or holding after rapid cooling, promote nucleation of pearlite block particles, It can be 20 μm or less.

  Here, the average block particle size of pearlite is that the L section of the wire is embedded in resin and cut and polished, and the region surrounded by the interface with a magnification of 500 times and an orientation difference of 9 ° is defined as one block particle by EBSP analysis. Analysis was performed and the average particle size was determined from the average volume.

  As means for controlling the area ratio of the pro-eutectoid ferrite and bainite and the average block particle size of the pearlite structure as described above, the steel slab is hot-rolled at a finish rolling temperature of 1000 to 1200 ° C, and then 880 ° C. After winding at a temperature of 960 ° C. or lower and after immersing in a molten salt of 520 ° C. or higher and 580 ° C. or lower for 30 seconds or more, or after winding under the above conditions, by means such as local blast , A method of performing a patenting treatment in which the cooling rate from 800 ° C. to 600 ° C. is 50 ° C./s or more and 200 ° C./s or less, and then maintained at a temperature range of 520 to 580 ° C. for 30 s or more. Adopted.

  The hot rolling and coiling conditions are within the above range because the rolled γ grain size is increased and B is present in the austenite in a solid solution state, and such B is concentrated at the grain boundary and is first precipitated. This is because the effect of suppressing the precipitation of ferrite is exhibited.

  When the finishing temperature of hot rolling is less than 1000 ° C., the rolling reaction force increases, and the γ grain size becomes finer, so that the hardenability is lowered and the area ratio of pro-eutectoid ferrite is increased. On the other hand, when it exceeds 1200 ° C., it becomes difficult to control the winding temperature to a specified temperature. Therefore, it is defined as 1000 ° C. or more and 1200 ° C. or less.

  When the coiling temperature is less than 880 ° C., B precipitates as carbides, and the effect of suppressing the precipitation of pro-eutectoid ferrite becomes insufficient, and when it exceeds 960 ° C., the γ particle size becomes excessively coarse.

The reason why the temperature of the molten salt or the holding temperature during cooling is limited to the temperature range of 520 to 580 ° C. is to make the area ratio of proeutectoid ferrite and bainite within the range defined by the above formula 2, and less than 520 ° C. Then, the amount of upper bainite increases rapidly, and if it is higher than 580 ° C., the amount of proeutectoid ferrite increases rapidly.
In addition, when not immersed in the molten salt, cooling is performed so that the cooling rate from 800 ° C. to 600 ° C. is 50 ° C./s or more and 200 ° C./s or less, similar to the cooling rate when immersed in the molten salt. This is to achieve a cooling rate.

As a result, both the pro-eutectoid ferrite and bainite are suppressed, and the remaining 95% or more has a pearlite structure, and the pearlite block particle size usually exceeds 20 μm due to the promotion of nucleation by rapid cooling after winding. Can be reduced to 20 μm or less.
FIG. 5 shows a SEM observation photograph of a typical pearlite structure of the rolled wire rod according to the present invention.

  The lamella spacing of pearlite depends on the temperature at the time of transformation, and if the temperature fluctuation is large, it becomes difficult to obtain pearlite with continuous lamellae. This tendency is particularly remarkable in the medium carbon steel of 0.3 to 0.5% C. In normal stealmore, only a breeze is produced and recuperation due to the latent heat of transformation when pearlite transformation proceeds cannot be suppressed, so it is difficult to keep the temperature during transformation constant.

  In contrast, when directly immersed in the molten salt, the heat removal ability is high, so the wire temperature at the time of transformation can be kept constant at a temperature close to the salt temperature, as shown in FIG. A pearlite structure in which the lamella structure is almost continuous can be obtained. The same applies to the case where the temperature is kept constant after forcibly cooling.

Furthermore, the wire drawing conditions and the steel wire conditions after drawing will be described.
Rolled wire that has been manufactured under the above manufacturing conditions and has been subjected to in-line patenting that satisfies the above-described component composition, structure, and strength conditions, and thereafter is not subjected to any heat treatment such as patenting or blueing. Thus, by performing cold wire drawing with a true strain of 4 or more so that the diameter D is 0.2 mm or more and 0.4 mm or less, the tensile strength TS (MPa) is 3000 MPa or more and Use ultra fine steel wire to satisfy.
3950−D × 2600 ≦ TS (Formula 3)

In consideration of the recent demand for high-strength materials for improving fuel efficiency, desirable TS is a level that satisfies the following formula 4.
4100−D × 2600 ≦ TS (Formula 4)
By doing in this way, as shown in FIG. 2, it becomes possible to obtain a steel wire having high strength and no occurrence of delamination.

Here, the true strain was set to 4 or more in order to obtain a steel wire having a target wire diameter of 0.2 to 0.4 mm from the rolled wire diameter of the present invention. Because.
Note that one or more lubrication treatments are required to perform drawing with a true strain of 4 or more. For this reason, it is advisable to carry out a lubricating film treatment that does not require bluing such as electric brass plating using a cyan bath, powder coating of brass, and a bond treatment.

After hot rolling the test material having the chemical composition shown in Table 1, it was wound at various winding temperatures and immediately immersed in molten salt at various temperatures, or by local blast from 800 ° C. Forcibly cooled so that the cooling rate to 600 ° C. is 50 ° C./s or more and 200 ° C./s or less, and patenting (test steel No. 8) is held at a constant temperature, and the diameter is 3.8 to A 6.7 mm wire was obtained. The test steel No. No. 16 was gradually cooled after winding. Thereafter, these wires were drawn to a diameter of 0.2 to 0.4 mm without re-patenting and bluing to obtain steel wires.
The tensile strength of the obtained wire and steel wire was examined by a tensile test, and the delamination characteristics of the steel wire were examined by a twist test. The results are shown in Table 2.

1 to 15 in Tables 1 and 2 are examples of the present invention, and others are comparative examples. As can be seen from the table, all the examples of the present invention have the TS of the rolled wire rod as the following formula 1
1000 × (% C) + 350 ≦ TS (MPa) ≦ 1000 × (% C) +500
The area ratio FA (%) of pro-eutectoid ferrite and bainite is expressed by the following formula 2.
0 ≦ FA ≦ −35 × (% C) +22
When the wire is drawn to a diameter of 0.2 to 0.4 mm with a true strain of 4 or more, the tensile strength is expressed by the following formula 3
3950-D × 2600 ≦ TS (MPa)
And delamination does not occur.

In contrast, the comparative example has the following problems.
No. 16 was an example in which the TS of the rolled wire rod was low and the target TS could not be secured after wire drawing because the inline heat treatment after rolling was performed by blast cooling with stealmore, and the ferrite + bainite fraction could not be suppressed. is there.

Examples 17 and 18 are examples where the final rolling temperature and the coiling temperature were low, so that the rolled γ grain size was reduced and the ferrite + bainite fraction could not be suppressed.
19 and 20 are examples in which the TS of the rolled wire is high because the amount of C is too high, and the ductility deteriorates during wire drawing, and 21 and 22 are examples in which the TS of the rolled wire is low because the C amount is low. This is an example in which the target TS could not be secured after wire drawing.

  No. 23 is an example in which a large amount of bainite was generated because the salt temperature during the melted salt treatment was too low. No. 24 is an example in which the B content was too small, and the ferrite + bainite fraction was high, and 25 was an excessive amount of B, so there was much precipitation of B carbonitride, and the effect of B addition (reduction of the ferrite + bainite fraction) This is an example that could not be obtained.

  A steel wire excellent in mechanical properties such as strength and tensile strength that can be produced without performing patenting and bluing treatment during the wire drawing process, and a wire for producing the steel wire, and methods for producing the same The industrial effect is extremely remarkable.

Claims (6)

% By mass, ppm by mass, C: 0.30 to 0.50%, Si: 0.10 to 0.40%, Mn: 0.20 to 1.0%, B: 4 to 30 ppm, N: 15 Contains 35 ppm, O: 15-35 ppm, Al: 0.01% or less (including 0%), Ti: 0.01% or less (including 0%), and consists of the balance iron and unavoidable impurities, patenting Later tensile strength TS (MPa) is in the range of the following formula 1,
1000 × (% C) + 350 ≦ TS ≦ 1000 × (% C) +500
... (Formula 1)
And the area ratio FA (%) of pro-eutectoid ferrite and bainite is in the range of the following formula 2,
FA ≦ −35 × (% C) +22 (Formula 2)
95% or more of the balance is a pearlite structure, and the average block particle size of the pearlite structure is 20 μm or less, a wire rod for high strength steel wire having a wire diameter of 3.6 to 7 mm.   Furthermore, in mass%, Cr: 0.5% or less, Ni: 0.5% or less, Co: 0.5% or less, Cu: 0.2% or less, Mo: 0.2% or less, W: 0.0. The wire for high-strength steel wire according to claim 1, comprising at least one selected from the group consisting of 2% or less. A steel wire having a diameter D (mm) of 0.2 to 0.4 mm by drawing the wire according to claim 1 or 2 without performing a heat treatment, wherein the tensile strength TS (MPa ) Is 3000 MPa or more, and satisfies the following formula 3. A high-strength ultrafine steel wire free from delamination.
3950−D × 2600 ≦ TS (Formula 3)   The steel slab of the steel component according to claim 1 or 2 is hot-rolled, the finish rolling temperature is 1000 to 1200 ° C, and then wound at a temperature of 880 to 960 ° C. The method for producing a high-strength steel wire according to claim 1 or 2, wherein a patenting treatment including a step of immersing in a molten salt for 30 seconds or more is performed.   The steel slab of the steel component according to claim 1 or 2 is hot-rolled, the finish rolling temperature is 1000 to 1200 ° C, and then wound at a temperature of 880 to 960 ° C, and then 800 ° C to 600 ° C. The high-strength steel according to claim 1 or 2, wherein the cooling rate is set to 50 to 200 ° C / s, and thereafter a patenting process including a step of holding at a temperature range of 520 to 580 ° C for 30 s or more is performed. A method for manufacturing a wire rod.   The wire rod manufactured by the method according to claim 4 or 5 is stretched until the diameter D (mm) is in a range of 0.2 to 0.4 mm under a condition of a true strain of 4% or more without performing heat treatment. The method for producing a high-strength ultrafine steel wire according to claim 3, wherein the wire is formed.