CN117327883B - Non-quenched and tempered steel wire rod and production method thereof - Google Patents

Non-quenched and tempered steel wire rod and production method thereof Download PDF

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Publication number
CN117327883B
CN117327883B CN202311631350.3A CN202311631350A CN117327883B CN 117327883 B CN117327883 B CN 117327883B CN 202311631350 A CN202311631350 A CN 202311631350A CN 117327883 B CN117327883 B CN 117327883B
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wire rod
salt bath
continuous casting
rolling
quenched
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CN117327883A (en
Inventor
于学森
麻晗
张宇
李战卫
陈茜
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Jiangsu Shagang Group Co Ltd
Jiangsu Shagang Iron and Steel Research Institute Co Ltd
Zhangjiagang Rongsheng Special Steel Co Ltd
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Jiangsu Shagang Group Co Ltd
Jiangsu Shagang Iron and Steel Research Institute Co Ltd
Zhangjiagang Rongsheng Special Steel Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/20—Recycling

Abstract

The invention discloses a non-quenched and tempered steel wire rod and a production method thereof. In the wire rod, 0.15-0.30% of C, 0.03-0.10% of Si, 0.6-0.8% of Mn, 0.0005-0.0035% of B, 0.01-0.03% of Ti, 0.015-0.055% of Al, less than or equal to 0.025% of S, less than or equal to 0.020% of P, less than or equal to 0.004% of N, and the balance of Fe and impurities, wherein Ceq=0.25-0.43%; the production method comprises the procedures of molten steel smelting, continuous casting, high-line rolling and salt bath which are sequentially carried out; the heating temperature of high-line rolling is 1060-1100 ℃, the initial rolling temperature is 940-970 ℃, and the spinning temperature is 800-860 ℃; in salt bath, the temperature of the salt bath tank is 400-500 ℃, and the salt bath time is 180-600 s. The wire rod has excellent mechanical properties and omits a quenching and tempering process.

Description

Non-quenched and tempered steel wire rod and production method thereof
Technical Field
The invention belongs to the technical field of steel smelting, relates to a production method of a non-quenched and tempered steel wire rod, and further relates to a non-quenched and tempered steel wire rod prepared by the production method.
Background
Compared with the traditional quenched and tempered steel, the non-quenched and tempered steel omits the quenching and tempering process, and reduces the environmental pollution caused by quenching and tempering heat treatment.
However, the existing non-quenched and tempered steel is usually prepared by improving C, mn or Cr and adding Nb, V, ni and the like for composite microalloying, so that the strength and plasticity of the steel are improved, the alloy cost is high, the requirements on rolling capacity, cooling process and the like of a rolling mill are extremely strict, defects are easily generated on the surface of a continuous casting blank, and the comprehensive performance of a finally prepared wire rod is not facilitated.
Disclosure of Invention
The invention aims to provide a production method of a non-quenched and tempered steel wire rod and the non-quenched and tempered steel wire rod prepared by the method.
In order to achieve one of the above objects, an embodiment of the present invention provides a method for producing a non-quenched and tempered steel wire rod, wherein the wire rod comprises the following chemical components in percentage by mass: 0.15-0.30% of C, 0.03-0.10% of Si, 0.6-0.8% of Mn, 0.0005-0.0035% of B, 0.01-0.03% of Ti, 0.015-0.055% of Al, less than or equal to 0.025% of S, less than or equal to 0.020% of P, less than or equal to 0.004% of N, the balance of Fe and other unavoidable impurities, and a carbon equivalent Ceq=0.25-0.43%;
the production method comprises the procedures of molten steel smelting, continuous casting, high-line rolling and salt bath which are sequentially carried out;
in the high-line rolling process, heating the billet or intermediate billet obtained in the continuous casting process, and then sequentially performing rough rolling and finish rolling, wherein the heating temperature is 1060-1100 ℃, the initial rolling temperature of rough rolling is 940-970 ℃, the finish rolling inlet temperature is 830-850 ℃, and the spinning temperature is 800-860 ℃;
in the salt bath process, the temperature of a salt bath tank is 400-500 ℃, and the salt bath time is 180-600 s.
As a further improvement of an embodiment of the present invention, the chemical components of the wire rod include, in mass percent: 0.15-0.30% of C, 0.03-0.10% of Si, 0.6-0.8% of Mn, 0.0005-0.0035% of B, 0.01-0.03% of Ti, 0.015-0.055% of Al, 0.010-0.025% of S, less than or equal to 0.020% of P, less than or equal to 0.004% of N, the balance of Fe and other unavoidable impurities, and a carbon equivalent Ceq=0.25-0.43%.
As a further improvement of an embodiment of the present invention, in the high-line rolling process, the spinning temperature is 800-840 ℃;
in the salt bath process, the wire rods after spinning are directly immersed into a salt bath tank to carry out salt bath, wherein the salt bath time is 180-600 s.
As a further improvement of an embodiment of the present invention, the method for producing a non-quenched and tempered steel wire rod further includes a stelmor cooling process performed after the high-pass rolling process; and is also provided with
In the high-speed wire rolling process, the wire laying temperature is 840-860 ℃;
in the step of cooling, the speed of a roller way at an inlet section is 0.8-1.5 m/s, and a heat preservation cover on a cooling line of the Steyr is fully opened;
in the salt bath process, the wire rod obtained in the stelmor cooling process is pickled to remove iron scales on the surface of the wire rod before salt bath, then the wire rod is heated to 900-930 ℃, and then the wire rod is immersed into a salt bath tank to be subjected to salt bath, wherein the paying-off speed is controlled to be 1.0-3.0 m/min, and the salt bath time is 200-600 s.
In the continuous casting step, a bloom with a cross-sectional dimension of 240mm×300mm×390mm is obtained by continuous casting, and the bloom is formed into an intermediate bloom with a cross-sectional dimension of 140mm×140mm×200mm before the high-pass rolling step, and the heating temperature of the bloom is 1160-1200 ℃.
As a further improvement of an embodiment of the invention, in the continuous casting process, the superheat degree of molten steel is controlled to be 30-35 ℃, the stirring current of a crystallizer is 700+/-50A, the stirring frequency of the crystallizer is 1.5+/-0.1 Hz, the pulling speed during continuous casting is 0.6+/-0.1 m/min, the specific water quantity of continuous casting is 0.15+/-0.01L/kg, and the rolling reduction is 11-13 mm under light pressure.
As a further improvement of an embodiment of the invention, in the continuous casting process, billet continuous casting is adopted to obtain billets with the cross section dimension of 140mm multiplied by 140mm to 200mm multiplied by 200mm, the superheat degree of molten steel is controlled to be 20 to 25 ℃, the stirring current of a crystallizer is 300+/-25A, the stirring frequency of the crystallizer is 4+/-0.5 Hz, the pulling speed during continuous casting is 2.6+/-0.1 m/min, the specific water quantity of continuous casting is 1.23+/-0.01L/kg, the stirring current at the tail end is 400+/-25A, and the stirring frequency at the tail end is 12+/-0.5 Hz.
In order to achieve one of the above objects, an embodiment of the present invention further provides a non-quenched and tempered steel wire rod, which is manufactured by the method for manufacturing a non-quenched and tempered steel wire rod as described above.
As a further improvement of an embodiment of the invention, the metallographic structure of the wire rod is bainite+ferrite, wherein the content of bainite is more than or equal to 85 percent, and the content of ferrite is less than 15 percent; the diameter of the wire rod is 8-18 mm, the tensile strength is 620-725 MPa, and the area shrinkage is 75-85%.
As a further improvement of an embodiment of the invention, the wire rod can be subjected to drawing processing with a reduction of 20-65%, and the tensile strength of the wire rod after the drawing processing is 900-1505 MPa, and the reduction of area is more than or equal to 30%.
Compared with the prior art, the non-quenched and tempered steel wire rod and the production method thereof have the beneficial effects that:
(1) Based on the design scheme of the chemical components, the content of C, mn and the range of carbon equivalent Ceq are controlled, the content of Si is limited, the hardenability of steel is further improved by adding B, the strength is further improved by adding Ti, N is fixed by adding Ti, BN is prevented from being formed, the hardenability of B is fully exerted, in addition, ti and C can form TiC, and tiny TiN and TiC have fine-grain strengthening effect on the steel, so that the strength and plasticity of the steel can be improved, the loss of solid solution strengthening of the steel due to low content of C, si and Mn is compensated, and a foundation is laid for the wire rod with good hardenability and welding performance;
(2) Based on the design scheme of the chemical components and the control of production processes such as continuous casting, rolling, salt bath and the like, the homogeneity of the steel is improved, and the metallographic structure of the wire rod prepared by adopting the production method is bainite+ferrite, wherein the content of bainite is more than or equal to 85%, and the content of ferrite is less than 15%; when the diameter of the wire rod is 8-18 mm, the tensile strength is 620-725 MPa, the area reduction rate is 75-85%, and the wire rod has higher strength and good plasticity;
(3) The wire rod can be subjected to drawing processing with the reduction rate of 20-65%, the tensile strength of the wire rod after the drawing processing is 900-1505 MPa, and the area reduction rate is more than or equal to 30%. That is, the strength of the wire rod can be further improved through drawing, and the wire rod after the drawing has good plasticity, so that the requirement of cold heading deformation can be met; the invention omits the quenching and tempering process, reduces the production process, effectively reduces the production cost and meets the environmental protection requirement.
Drawings
Fig. 1 shows a metallographic structure picture of the wire rod of example 1;
fig. 2 shows a metallographic structure picture of the wire rod of example 2;
fig. 3 shows a metallographic structure picture of the wire rod of example 3;
fig. 4 shows a metallographic structure picture of the wire rod of example 4;
FIG. 5 shows photographs of iron pieces from which wire rods obtained in examples 1, 2 and 4 were removed after turning;
fig. 6 shows a photograph of iron filings from which the wire rods obtained in example 3 were removed after turning.
Detailed Description
The technical scheme of the present invention will be further described with reference to the specific embodiments, but the scope of the claims is not limited to the description.
The invention provides a production method of a non-quenched and tempered steel wire rod and the non-quenched and tempered steel wire rod prepared by the production method.
The non-quenched and tempered steel wire rod comprises the following chemical components in percentage by mass: 0.15-0.30% of C, 0.03-0.10% of Si, 0.6-0.8% of Mn, 0.0005-0.0035% of B, 0.01-0.03% of Ti, 0.015-0.055% of Al, less than or equal to 0.025% of S, less than or equal to 0.020% of P, less than or equal to 0.004% of N, the balance of Fe and other unavoidable impurities, and a carbon equivalent Ceq=0.25-0.43%.
In the chemical composition of the invention:
c is the most basic strengthening element in the steel, but as the content of C is increased, the plasticity of the wire rod is deteriorated, the cold heading performance is also deteriorated, and when the content of C exceeds 0.3%, the welding performance of the steel is also deteriorated, wherein the content of C is limited to 0.15-0.30%.
Si is a strengthening element and a deoxidizing element in steel, but excessive Si can reduce the plasticity and cold heading performance of the wire rod, and the Si content is limited to 0.03-0.10%.
Mn is a strengthening element in steel, so that the strength and hardenability of the steel can be improved, but excessive Mn can reduce the plasticity and welding performance of the steel, and the Mn content is limited to 0.6-0.8%.
B can improve the hardenability of steel and achieve the purpose of improving strength, but B content is too high and forms a 'boron phase' at a grain boundary, so that the plasticity of the steel is reduced, and the B content is limited to 0.0005-0.0035%.
Ti can form fine TiC and TiN in the steel, so that B and N in the steel are prevented from forming BN, the B fully plays a role in improving hardenability, and in addition, fine TiC and TiN can refine grains, so that the strength and plasticity of the steel are improved. However, too high Ti content coarsens TiN and TiC, which is unfavorable for fine grain strengthening and continuous casting production. The Ti content in the invention is limited to 0.01-0.03%.
Al is a deoxidizing element in steel, can effectively remove oxygen in the steel, improves the cleanliness of the steel, and can also form AlN with N to refine grains.
S is easily deviated in grain boundaries to embrittle the grain boundaries, thereby reducing the strength and plasticity of steel, and S and Mn form MnS, thereby reducing the solid solution strengthening effect of Mn, and the S content is limited to be less than or equal to 0.025 percent in the invention.
P is an impurity element in steel, and tends to be concentrated in grain boundaries to embrittle the grain boundaries, and further, strength and plasticity of steel are reduced, and the P content is limited to 0.020% or less in the present invention.
N can cause the plasticity of steel to be poor, the cold heading performance of the steel is affected, alN and TiN are coarsened due to high N content, fine grain strengthening is not facilitated, and the nitrogen content is limited to be less than or equal to 0.004%.
Carbon equivalent ceq=c+mn/6, and in the present invention, the carbon equivalent Ceq is controlled to be 0.25 to 0.43% so that the steel has good weldability.
Based on the design scheme of the chemical components, the content of C, mn and the range of carbon equivalent Ceq are controlled, the content of Si is limited, the hardenability of steel is further improved by adding B, the strength is further improved, ti is added to form TiN for fixing N and preventing BN from being formed, so that the B fully plays the role of improving the hardenability, in addition, ti and C can form TiC, and tiny TiN and TiC have the function of fine-grained strengthening on the steel, so that the strength and plasticity of the steel can be improved, the loss of solid solution strengthening of the steel due to low content of C, si and Mn is compensated, and a foundation is laid for the wire rod having good hardenability and welding performance.
Preferably, the chemical components of the non-quenched and tempered steel wire rod comprise the following components in percentage by mass: 0.15-0.30% of C, 0.03-0.10% of Si, 0.6-0.8% of Mn, 0.0005-0.0035% of B, 0.01-0.03% of Ti, 0.015-0.055% of Al, 0.010-0.025% of S, less than or equal to 0.020% of P, less than or equal to 0.004% of N, the balance of Fe and other unavoidable impurities, and a carbon equivalent Ceq=0.25-0.43%.
In the preferred chemical composition design scheme, the S content is controlled to be 0.010-0.025%, and the method is suitable for deep processing of wire rods needing turning.
In addition, when the method is applied to the wire rod which does not need turning and has the requirement of cold heading large deformation, the S content is preferably controlled to be S <0.010 percent so as not to damage the performance of the wire rod due to the excessively high S content.
The following describes a preferred method of producing the non-quenched and tempered steel wire rod of the present invention by means of two embodiments.
First embodiment
The production method of the non-quenched and tempered steel wire rod comprises the following steps of:
(1) Molten steel smelting process
Smelting molten steel through sequentially carrying out converter smelting and LF refining steps, so that the chemical components of molten steel at a smelting end point meet the following mass percent: 0.15-0.30% of C, 0.03-0.10% of Si, 0.6-0.8% of Mn, 0.0005-0.0035% of B, 0.01-0.03% of Ti, 0.015-0.055% of Al, less than or equal to 0.025% of S, less than or equal to 0.020% of P, less than or equal to 0.004% of N, the balance of Fe and other unavoidable impurities, and a carbon equivalent Ceq=0.25-0.43%.
Correspondingly, the chemical components of the molten steel at the smelting end point are preferably satisfied to comprise in mass percent: 0.15-0.30% of C, 0.03-0.10% of Si, 0.6-0.8% of Mn, 0.0005-0.0035% of B, 0.01-0.03% of Ti, 0.015-0.055% of Al, 0.010-0.025% of S, less than or equal to 0.020% of P, less than or equal to 0.004% of N, the balance of Fe and other unavoidable impurities, and a carbon equivalent Ceq=0.25-0.43%. Therefore, the finally prepared non-quenched and tempered steel wire rod is suitable for application scenes of deep processing requiring turning.
In the converter smelting step, molten iron is sent into a converter to be mixed with scrap steel into molten steel, desilication, dephosphorization, oxygen blowing and decarburization are carried out, and alloy is added into a steel ladle for deoxidization alloying during tapping; in the refining step, molten steel smelted by a converter is sent into an LF refining furnace for chemical component adjustment and temperature regulation, and inclusions in the molten steel are regulated and controlled through soft stirring until the temperature and the chemical components reach standards, and then tapping is carried out.
It is understood that the chemical composition of molten steel obtained in the molten steel smelting process and the chemical composition of a continuous casting blank obtained in the continuous casting process are consistent with the chemical composition of the non-quenched and tempered steel wire rod finally prepared by the production method.
(2) Continuous casting process
And casting the molten steel obtained in the molten steel smelting process into a continuous casting blank. The method can be carried out in the following two modes:
in the first mode, small square billets with the cross section size of 140mm multiplied by 140mm to 200mm multiplied by 200mm are obtained by continuous casting, and can be directly rolled in a high-line mode, so that the working procedures are saved, and the production cost is reduced; the superheat degree of molten steel is controlled to be 20-25 ℃, the stirring current of a crystallizer is 300+/-25A, the stirring frequency of the crystallizer is 4+/-0.5 Hz, the pulling speed during continuous casting is 2.6+/-0.1 m/min, the specific water quantity of continuous casting is 1.23+/-0.01L/kg, the terminal stirring current is 400+/-25A, and the terminal stirring frequency is 12+/-0.5 Hz.
The center segregation index of the prepared billet is less than 1.05 by controlling the parameters of the continuous casting process.
And secondly, continuous casting is carried out on the large square billet to obtain a large square billet with the cross section dimension of 240mm multiplied by 300mm multiplied by 390mm, the large square billet is cogged into an intermediate billet with the cross section dimension of 140mm multiplied by 200mm before the high-speed wire rolling process, and the heating temperature of cogging is controlled to be 1160 ℃ to 1200 ℃. Thus, the segregation can be reduced, the tissue uniformity of the continuous casting blank is improved, and the large square blank does not need to be put into a pit for slow cooling.
Preferably, the superheat degree of molten steel is controlled to be 30-35 ℃, the stirring current of a crystallizer is 700+/-50A, the stirring frequency of the crystallizer is 1.5+/-0.1 Hz, the pulling speed during continuous casting is 0.6+/-0.1 m/min, the specific water quantity during continuous casting is 0.15+/-0.01L/kg, the continuous casting adopts light reduction, and the reduction is 11-13 mm. By controlling the parameters of the continuous casting process, the center segregation index of the prepared intermediate billet is less than 1.03, and the tissue uniformity is greatly improved.
The center segregation index is a ratio of the C content at the center of the cross section of the billet or the intermediate billet to the C content in the molten steel at the smelting end point.
(3) High-speed wire rolling process
And heating the small square billet or the intermediate billet obtained in the continuous casting process, and then performing rough rolling and finish rolling to prepare the wire rod, wherein the heating temperature is 1060-1100 ℃, the initial rolling temperature of rough rolling is 940-970 ℃, the finish rolling inlet temperature is 830-850 ℃, and the spinning temperature is 800-860 ℃.
Preferably, the laying temperature is 800-840 ℃.
(4) Salt bath process
The temperature of the salt bath is 400-500 ℃, and the salt bath time is 180-600 s.
Preferably, the wire rods after spinning are directly immersed into a salt bath tank for salt bath, and the salt bath time is 180-250 s.
According to the embodiment, the component segregation of the continuous casting billet can be effectively reduced through the control of the continuous casting process, the abnormal growth of crystal grains can be effectively restrained through the optimal design of chemical components and the control of various process parameters in the high-line rolling process, the crystal grains are refined and uniform, the wire rods obtained after spinning can directly enter a salt bath tank for salt bath treatment without reheating, the production flow is saved, the production cost is reduced, the environment is protected, the structure of the wire rods is optimized, the wire rod structure is a uniform bainite+ferrite structure, other abnormal structures such as pearlite and martensite are avoided, and the strength and plasticity of the wire rods are effectively improved.
Second embodiment
The production method of the non-quenched and tempered steel wire rod comprises the following steps of:
(1) Molten steel smelting process
Smelting molten steel through sequentially carrying out converter smelting and LF refining steps, so that the chemical components of molten steel at a smelting end point meet the following mass percent: 0.15-0.30% of C, 0.03-0.10% of Si, 0.6-0.8% of Mn, 0.0005-0.0035% of B, 0.01-0.03% of Ti, 0.015-0.055% of Al, less than or equal to 0.025% of S, less than or equal to 0.020% of P, less than or equal to 0.004% of N, the balance of Fe and other unavoidable impurities, and a carbon equivalent Ceq=0.25-0.43%.
Correspondingly, the chemical components of the molten steel at the smelting end point are preferably satisfied to comprise in mass percent: 0.15-0.30% of C, 0.03-0.10% of Si, 0.6-0.8% of Mn, 0.0005-0.0035% of B, 0.01-0.03% of Ti, 0.015-0.055% of Al, 0.010-0.025% of S, less than or equal to 0.020% of P, less than or equal to 0.004% of N, the balance of Fe and other unavoidable impurities, and a carbon equivalent Ceq=0.25-0.43%. Therefore, the finally prepared non-quenched and tempered steel wire rod is suitable for application scenes of deep processing requiring turning.
In the converter smelting step, molten iron is sent into a converter to be mixed with scrap steel into molten steel, desilication, dephosphorization, oxygen blowing and decarburization are carried out, and alloy is added into a steel ladle for deoxidization alloying during tapping; in the refining step, molten steel smelted by a converter is sent into an LF refining furnace for chemical component adjustment and temperature regulation, and inclusions in the molten steel are regulated and controlled through soft stirring until the temperature and the chemical components reach standards, and then tapping is carried out.
It is understood that the chemical composition of molten steel obtained in the molten steel smelting process and the chemical composition of a continuous casting blank obtained in the continuous casting process are consistent with the chemical composition of the non-quenched and tempered steel wire rod finally prepared by the production method.
(2) Continuous casting process
And casting the molten steel obtained in the molten steel smelting process into a continuous casting blank. The method can be carried out in the following two modes:
in the first mode, small square billets with the cross section size of 140mm multiplied by 140mm to 200mm multiplied by 200mm are obtained by continuous casting, and can be directly rolled in a high-line mode, so that the working procedures are saved, and the production cost is reduced; the superheat degree of molten steel is controlled to be 20-25 ℃, the stirring current of a crystallizer is 300+/-25A, the stirring frequency of the crystallizer is 4+/-0.5 Hz, the pulling speed during continuous casting is 2.6+/-0.1 m/min, the specific water quantity of continuous casting is 1.23+/-0.01L/kg, the terminal stirring current is 400+/-25A, and the terminal stirring frequency is 12+/-0.5 Hz.
The center segregation index of the prepared billet is less than 1.05 by controlling the parameters of the continuous casting process.
And secondly, continuous casting is carried out on the large square billet to obtain a large square billet with the cross section dimension of 240mm multiplied by 300mm multiplied by 390mm, the large square billet is cogged into an intermediate billet with the cross section dimension of 140mm multiplied by 200mm before the high-speed wire rolling process, and the heating temperature of cogging is controlled to be 1160 ℃ to 1200 ℃. Thus, the segregation can be reduced, the tissue uniformity of the continuous casting blank is improved, and the large square blank does not need to be put into a pit for slow cooling.
Preferably, the superheat degree of molten steel is controlled to be 30-35 ℃, the stirring current of a crystallizer is 700+/-50A, the stirring frequency of the crystallizer is 1.5+/-0.1 Hz, the pulling speed during continuous casting is 0.6+/-0.1 m/min, the specific water quantity during continuous casting is 0.15+/-0.01L/kg, the continuous casting adopts light reduction, and the reduction is 11-13 mm. By controlling the parameters of the continuous casting process, the center segregation index of the prepared intermediate billet is less than 1.03, and the tissue uniformity is greatly improved.
(3) High-speed wire rolling process
And heating the small square billet or the intermediate billet obtained in the continuous casting process, and then performing rough rolling and finish rolling to prepare the wire rod, wherein the heating temperature is 1060-1100 ℃, the initial rolling temperature of rough rolling is 940-970 ℃, the finish rolling inlet temperature is 830-850 ℃, and the spinning temperature is 800-860 ℃.
Preferably, the laying temperature is 840-860 ℃.
(4) Stelmor cooling process
And (3) performing temperature control cooling on the rolled wire rod by adopting a Steyr cooling line, wherein the roller speed of the inlet section is 0.8-1.5 m/s, and the heat preservation cover on the Steyr cooling line is fully opened.
(5) Salt bath process
The temperature of the salt bath is 400-500 ℃, and the salt bath time is 180-600 s.
Preferably, the coil rod obtained in the step of cooling by stelmor is pickled before salt bath, oxidized iron scales on the surface of the coil rod are removed, then the coil rod is heated to 900-930 ℃, and then the coil rod is immersed into a salt bath tank for salt bath, the paying-off speed is controlled to be 1.0-3.0 m/min, and the salt bath time is 200-600 s.
According to the embodiment, the wire rods are cooled on the Steyr cooling line after being rolled by the high line, and low-speed slow cooling is not required to be kept, so that the roller speed can be improved, the stacking thickness of the wire rods is thinner, the scratch probability among the wire rods is reduced, the surface quality of the wire rods is improved, the production efficiency is improved, and the working strength of operators is reduced; furthermore, the salt bath of the embodiment is not affected by the temperature after high-line rolling and the like, the production rhythm is flexible, and sufficient time is provided for salt bath treatment, so that the control of the wire rod structure is facilitated, and the generation of abnormal structures is reduced.
In addition, the invention also provides a non-quenched and tempered steel wire rod, which is prepared by adopting the production method of the first embodiment or the second embodiment, wherein the wire rod comprises the following chemical components in percentage by mass: 0.15-0.30% of C, 0.03-0.10% of Si, 0.6-0.8% of Mn, 0.0005-0.0035% of B, 0.01-0.03% of Ti, 0.015-0.055% of Al, less than or equal to 0.025% of S, less than or equal to 0.020% of P, less than or equal to 0.004% of N, the balance of Fe and other unavoidable impurities, and a carbon equivalent Ceq=0.25-0.43%.
Preferably, the chemical components of the wire rod comprise the following components in percentage by mass: 0.15-0.30% of C, 0.03-0.10% of Si, 0.6-0.8% of Mn, 0.0005-0.0035% of B, 0.01-0.03% of Ti, 0.015-0.055% of Al, 0.010-0.025% of S, less than or equal to 0.020% of P, less than or equal to 0.004% of N, the balance of Fe and other unavoidable impurities, and Ceq=0.25-0.43% of carbon equivalent.
The metallographic structure of the wire rod is bainite+ferrite, wherein the content of bainite is more than or equal to 85%, and the content of ferrite is less than 15%.
The diameter of the wire rod is 8-18 mm, the tensile strength is 620-725 MPa, the area shrinkage is 75-85%, and the wire rod has higher strength and good plasticity.
The wire rod can be subjected to drawing processing with the reduction rate of 20-65%, the tensile strength of the wire rod after the drawing processing is 900-1505 MPa, and the area reduction rate is more than or equal to 30%. That is, the strength of the wire rod can be further improved by the drawing process, and the wire rod after the drawing process has good plasticity, and can meet the requirement of cold heading deformation. The invention omits the quenching and tempering process, reduces the production process, effectively reduces the production cost and meets the environmental protection requirement.
Wherein, the reduction ratio= (area of wire rod cross section before drawing-area of wire rod cross section after drawing)/area of wire rod cross section before drawing-100%.
The present invention has been achieved in accordance with a great deal of experimental study, and for the purpose, technical solutions and advantages of one embodiment of the present invention, the following will specifically describe the present embodiment in conjunction with examples 1 to 4 according to one embodiment of the present invention. It is apparent that embodiments 1-4 are described as only some, but not all, embodiments of the present invention.
The production method and wire rod of each embodiment are described in detail below.
Example 1
(1) Molten steel smelting process
Molten steel is smelted through the converter smelting and LF refining steps which are sequentially carried out, and the chemical components of molten steel at the smelting end point are shown in the following table 1 in percentage by mass. The chemical composition of the continuous cast slab obtained in the continuous casting step and the chemical composition of the non-quenched and tempered steel wire rod obtained in the final step were identical to those of the molten steel at the end of the molten steel melting step, and are shown in table 1.
In the converter smelting step, molten iron is sent into a converter to be mixed with scrap steel into molten steel, desilication, dephosphorization, oxygen blowing and decarburization are carried out, and alloy is added into a steel ladle for deoxidization alloying during tapping; in the refining step, molten steel smelted by a converter is sent into an LF refining furnace for chemical component adjustment and temperature regulation, and inclusions in the molten steel are regulated and controlled through soft stirring until the temperature and the chemical components reach standards, and then tapping is carried out.
(2) Continuous casting process
And casting the molten steel obtained in the molten steel smelting process into small square billets with the cross section dimension of 140mm multiplied by 140mm by adopting small square billet continuous casting.
Wherein the superheat degree of molten steel is controlled to 21 ℃, the stirring current of a crystallizer is 300+/-25A, the stirring frequency of the crystallizer is 4+/-0.5 Hz, the pulling speed during continuous casting is 2.6+/-0.1 m/min, the specific water quantity of continuous casting is 1.23+/-0.01L/kg, the terminal stirring current is 400+/-25A, and the terminal stirring frequency is 12+/-0.5 Hz.
(3) High-speed wire rolling process
And heating the small square billet obtained in the continuous casting process, and then performing rough rolling and finish rolling to prepare the wire rod with the diameter of 11mm, wherein the heating temperature is 1090 ℃, the initial rolling temperature of rough rolling is 950 ℃, the finish rolling inlet temperature is 830 ℃, and the spinning temperature is 810 ℃.
(4) Salt bath process
And directly immersing the wire rods subjected to spinning into a salt bath tank for salt bath, wherein the temperature of the salt bath tank is 450 ℃, and the salt bath time is 200s.
Example 2
(1) Molten steel smelting process
Molten steel is smelted through the converter smelting and LF refining steps which are sequentially carried out, so that the chemical components of molten steel at the smelting end point are shown in the following table 1 in percentage by mass. The chemical composition of the continuous cast slab obtained in the continuous casting step and the chemical composition of the non-quenched and tempered steel wire rod obtained in the final step were identical to those of the molten steel at the end of the molten steel melting step, and are shown in table 1.
In the converter smelting step, the pretreated molten iron is sent into a converter to be mixed with scrap steel into molten steel, desilication, dephosphorization, oxygen blowing and decarburization are carried out, and alloy is added into a steel ladle for deoxidization alloying during tapping; in the refining step, molten steel smelted by a converter is sent into an LF refining furnace for chemical component adjustment and temperature regulation, and inclusions in the molten steel are regulated and controlled through soft stirring until the temperature and the chemical components reach standards, and then tapping is carried out.
(2) Continuous casting process
And casting molten steel obtained in the molten steel smelting process into a bloom with the cross section size of 300mm multiplied by 390mm by adopting bloom continuous casting, cogging the bloom into an intermediate bloom with the cross section size of 140mm multiplied by 140mm before the high-speed rolling process, and controlling the cogging heating temperature to 1190 ℃.
Wherein the superheat degree of molten steel is controlled to 33 ℃, the stirring current of a crystallizer is 700+/-50A, the stirring frequency of the crystallizer is 1.5+/-0.1 Hz, the pulling speed during continuous casting is 0.6+/-0.1 m/min, the specific water quantity during continuous casting is 0.15+/-0.01L/kg, and the rolling reduction is 13mm under light rolling.
(3) High-speed wire rolling process
And (3) rolling the intermediate billet obtained in the continuous casting procedure into a wire rod with the diameter of 8mm by high-pass rolling, wherein the heating temperature is 1090 ℃, the initial rolling temperature of rough rolling is 960 ℃, the finish rolling inlet temperature is 845 ℃, and the spinning temperature is 855 ℃.
(4) Stelmor cooling process
And (3) performing temperature control cooling on the rolled wire rod by adopting a Steyr cooling line, wherein the roller speed of the inlet section is 1.0m/s, and the heat preservation covers on the Steyr cooling line are all opened.
(5) Salt bath process
And (3) pickling the wire rods obtained in the step of cooling by Steyr to remove iron scales on the surfaces of the wire rods before salt bath, heating to 925 ℃, immersing the wire rods in a salt bath tank to carry out salt bath, controlling the paying-off speed to be 2.0m/min, controlling the temperature of the salt bath tank to be 455 ℃, and controlling the salt bath time to be 300s.
Example 3
(1) Molten steel smelting process
Molten steel is smelted through the converter smelting and LF refining steps which are sequentially carried out, and the chemical components of molten steel at the smelting end point are shown in the following table 1 in percentage by mass. The chemical composition of the continuous cast slab obtained in the continuous casting step and the chemical composition of the non-quenched and tempered steel wire rod obtained in the final step were identical to those of the molten steel at the end of the molten steel melting step, and are shown in table 1.
In the converter smelting step, the pretreated molten iron is sent into a converter to be mixed with scrap steel into molten steel, desilication, dephosphorization, oxygen blowing and decarburization are carried out, and alloy is added into a steel ladle for deoxidization alloying during tapping; in the refining step, molten steel smelted by a converter is sent into an LF refining furnace for chemical component adjustment and temperature regulation, and inclusions in the molten steel are regulated and controlled through soft stirring until the temperature and the chemical components reach standards, and then tapping is carried out.
(2) Continuous casting process
And casting molten steel obtained in the molten steel smelting process into a bloom with the cross section size of 300mm multiplied by 390mm by adopting bloom continuous casting, cogging the bloom into an intermediate bloom with the cross section size of 140mm multiplied by 140mm before the high-speed wire rolling process, and controlling the cogging heating temperature to 1180 ℃.
Wherein, the superheat degree of molten steel is controlled to 34 ℃, the stirring current of a crystallizer is 700+/-50A, the stirring frequency of the crystallizer is 1.5+/-0.1 Hz, the pulling speed during continuous casting is 0.6+/-0.1 m/min, the specific water quantity during continuous casting is 0.15+/-0.01L/kg, and the rolling reduction is 12mm under light rolling.
(3) High-speed wire rolling process
And heating the intermediate billet obtained in the continuous casting process, and then performing rough rolling and finish rolling to prepare the wire rod with the diameter of 14mm, wherein the heating temperature is 1080 ℃, the initial rolling temperature of rough rolling is 945 ℃, the finish rolling inlet temperature is 840 ℃, and the spinning temperature is 825 ℃.
(4) Salt bath process
And directly immersing the wire rods subjected to spinning into a salt bath tank for salt bath, wherein the temperature of the salt bath tank is 455 ℃, and the salt bath time is 195s.
Example 4
(1) Molten steel smelting process
Molten steel is smelted through the converter smelting and LF refining steps which are sequentially carried out, so that the chemical components of molten steel at the smelting end point are shown in the following table 1 in percentage by mass. The chemical composition of the continuous cast slab obtained in the continuous casting step and the chemical composition of the non-quenched and tempered steel wire rod obtained in the final step were identical to those of the molten steel at the end of the molten steel melting step, and are shown in table 1.
In the converter smelting step, the pretreated molten iron is sent into a converter to be mixed with scrap steel into molten steel, desilication, dephosphorization, oxygen blowing and decarburization are carried out, and alloy is added into a steel ladle for deoxidization alloying during tapping; in the refining step, molten steel smelted by a converter is sent into an LF refining furnace for chemical component adjustment and temperature regulation, and inclusions in the molten steel are regulated and controlled through soft stirring until the temperature and the chemical components reach standards, and then tapping is carried out.
(2) Continuous casting process
And casting the molten steel obtained in the molten steel smelting process into small square billets with the cross section dimension of 140mm multiplied by 140mm by adopting small square billet continuous casting.
Wherein the superheat degree of molten steel is controlled to be 20 ℃, the stirring current of a crystallizer is 300+/-25A, the stirring frequency of the crystallizer is 4+/-0.5 Hz, the pulling speed during continuous casting is 2.6+/-0.1 m/min, the specific water quantity of continuous casting is 1.23+/-0.01L/kg, the terminal stirring current is 400+/-25A, and the terminal stirring frequency is 12+/-0.5 Hz.
(3) High-speed wire rolling process
And heating the small square billet obtained in the continuous casting process, and then performing rough rolling and finish rolling to prepare the wire rod with the diameter of 18mm, wherein the heating temperature is 1110 ℃, the initial rolling temperature of rough rolling is 965 ℃, the finish rolling inlet temperature is 845 ℃, and the spinning temperature is 850 ℃.
(4) Stelmor cooling process
And (3) performing temperature control cooling on the rolled wire rod by adopting a Steyr cooling line, wherein the roller speed of the inlet section is 0.8m/s, and the heat preservation covers on the Steyr cooling line are all opened.
(5) Salt bath process
And (3) pickling the wire rods obtained in the step of cooling by Steyr to remove iron scales on the surfaces of the wire rods before salt bath, heating to 920 ℃, immersing the wire rods in a salt bath tank to carry out salt bath, controlling the paying-off speed to be 1.5m/min, controlling the temperature of the salt bath tank to be 460 ℃, and controlling the salt bath time to be 400s.
TABLE 1
Sampling the wire rods of examples 1-4 according to the same test method, and detecting metallographic structure and mechanical property, wherein the specific test method and the detection result are as follows:
(1) In the aspect of metallographic structure, respectively taking wire rods with the length of 10cm from the head of the wire rod, preparing a metallographic sample, mechanically polishing, corroding with nitric alcohol, and then placing into a metallographic microscope for structural observation, wherein the structures of the wire rods in examples 1-4 are all bainitic+ferrite, the percentages of the bainitic and the ferrite are shown in table 2, and the metallographic structure pictures of the wire rods in examples 1-4 are shown in figures 1-4;
(2) In terms of mechanical properties, referring to GB/T228 standard test methods and definitions, a tensile tester is adopted to test the mechanical properties of the wire rods, and the tensile strength and the area shrinkage of the wire rods of examples 1-4 are respectively shown in Table 2;
(3) In the aspect of cutting performance, the same feed amount is adopted, the wire rods obtained in the embodiments 1-4 are turned by a lathe, the shape of the fallen scrap iron is observed, and in general, the smaller the length of the scrap iron is, the better the cutting performance of the wire rod is; the iron filings of the wire rods obtained in examples 1, 2 and 4, which are removed after turning, are shown in fig. 5, and as can be seen from fig. 5, the iron filings mainly comprise long iron filings, and the cutting performance of the wire rods is poor; the iron filings falling off after turning the wire rod obtained in the embodiment 3 are shown in fig. 6, and as can be seen from fig. 6, the iron filings mainly comprise short iron filings, which indicates that the cutting performance of the wire rod is better.
TABLE 2
Further, the wire rods of examples 1 to 4 were further drawn according to the reduction ratio shown in table 3, and the mechanical property test and 1/2 cold heading were performed on the drawn wire rods, and specific test methods and test results were as follows:
(1) In terms of mechanical properties, referring to GB/T228 standard test methods and definitions, a tensile tester is adopted to test mechanical properties, and the tensile strength and the area shrinkage of the wire rods of examples 1-4 after further drawing processing are respectively shown in Table 3;
(2) And (3) cold heading test, namely performing 1/2 cold heading test on the wire rod subjected to further drawing processing by referring to a YB/T5293 standard test method and definition.
TABLE 3 Table 3
In summary, it is known that the non-quenched and tempered steel wire rods of examples 1 to 4 produced according to the present embodiment have a metallographic structure of bainite+ferrite without quenching and tempering, wherein the content of bainite is not less than 85% and the content of ferrite is less than 15%; when the diameter of the wire rod is 8-18 mm, the tensile strength is 620-725 MPa, the area reduction rate is 75-85%, and the wire rod has higher strength and good plasticity; in addition, the wire rod can be subjected to drawing processing with the reduction rate of 20-65%, the tensile strength of the wire rod after the drawing processing is 900-1505 MPa, the area reduction rate is more than or equal to 30%, that is, the strength of the wire rod can be further improved through the drawing processing, the wire rod after the drawing processing still has good plasticity, and the requirement of cold heading deformation can be met.
The foregoing is only a preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art, who is within the scope of the present invention, shall cover the scope of the present invention according to the technical scheme of the present invention and the equivalents and modifications of the inventive concept thereof.

Claims (10)

1. The production method of the non-quenched and tempered steel wire rod is characterized by comprising the following chemical components in percentage by mass: 0.15-0.30% of C, 0.03-0.10% of Si, 0.6-0.8% of Mn, 0.0005-0.0035% of B, 0.01-0.03% of Ti, 0.015-0.055% of Al, less than or equal to 0.025% of S, less than or equal to 0.020% of P, less than or equal to 0.004% of N, the balance of Fe and other unavoidable impurities, and a carbon equivalent Ceq=0.25-0.43%;
the production method comprises the procedures of molten steel smelting, continuous casting, high-line rolling and salt bath which are sequentially carried out;
in the high-line rolling process, heating the billet or intermediate billet obtained in the continuous casting process, and then sequentially performing rough rolling and finish rolling, wherein the heating temperature is 1060-1100 ℃, the initial rolling temperature of rough rolling is 940-970 ℃, the finish rolling inlet temperature is 830-850 ℃, and the spinning temperature is 800-860 ℃;
in the salt bath process, the temperature of a salt bath tank is 400-500 ℃, and the salt bath time is 180-600 s.
2. The method for producing a non-quenched and tempered steel wire rod according to claim 1, wherein the chemical components of the wire rod include in mass percent: 0.15-0.30% of C, 0.03-0.10% of Si, 0.6-0.8% of Mn, 0.0005-0.0035% of B, 0.01-0.03% of Ti, 0.015-0.055% of Al, 0.010-0.025% of S, less than or equal to 0.020% of P, less than or equal to 0.004% of N, the balance of Fe and other unavoidable impurities, and a carbon equivalent Ceq=0.25-0.43%.
3. The method for producing a non-quenched and tempered steel wire rod according to claim 1, wherein,
in the high-speed wire rolling process, the spinning temperature is 800-840 ℃;
in the salt bath process, the wire rods after spinning are directly immersed into a salt bath tank to carry out salt bath, wherein the salt bath time is 180-600 s.
4. The method for producing a non-quenched and tempered steel wire rod according to claim 1, further comprising a stelmor cooling process performed after the high-pass rolling process; and is also provided with
In the high-speed wire rolling process, the wire laying temperature is 840-860 ℃;
in the step of cooling, the speed of a roller way at an inlet section is 0.8-1.5 m/s, and a heat preservation cover on a cooling line of the Steyr is fully opened;
in the salt bath process, the wire rod obtained in the stelmor cooling process is pickled to remove iron scales on the surface of the wire rod before salt bath, then the wire rod is heated to 900-930 ℃, and then the wire rod is immersed into a salt bath tank to be subjected to salt bath, wherein the paying-off speed is controlled to be 1.0-3.0 m/min, and the salt bath time is 200-600 s.
5. The method according to claim 1, wherein in the continuous casting step, a bloom having a cross-sectional dimension of 240mm x 300mm x 390mm is obtained by continuous casting of the bloom, and the bloom is formed into an intermediate bloom having a cross-sectional dimension of 140mm x 200mm before the high-pass rolling step, and the heating temperature of the bloom is 1160 ℃ to 1200 ℃.
6. The method for producing non-quenched and tempered steel wire rods according to claim 5, wherein in the continuous casting step, the superheat degree of molten steel is controlled to be 30-35 ℃, the stirring current of a crystallizer is 700+/-50A, the stirring frequency of the crystallizer is 1.5+/-0.1 Hz, the drawing speed during continuous casting is 0.6+/-0.1 m/min, the specific water content during continuous casting is 0.15+/-0.01L/kg, and the rolling reduction is 11-13 mm under light rolling.
7. The method according to claim 1, wherein in the continuous casting step, a billet is continuously cast to obtain a billet with a cross section of 140mm x 140mm to 200mm x 200mm, the superheat degree of molten steel is controlled to be 20 to 25 ℃, the stirring current of a crystallizer is controlled to be 300 + -25A, the stirring frequency of the crystallizer is controlled to be 4 + -0.5 Hz, the drawing speed during continuous casting is controlled to be 2.6 + -0.1 m/min, the specific water content during continuous casting is controlled to be 1.23 + -0.01L/kg, the terminal stirring current is controlled to be 400 + -25A, and the terminal stirring frequency is controlled to be 12 + -0.5 Hz.
8. A non-quenched and tempered steel wire rod characterized by being prepared by the production method of the non-quenched and tempered steel wire rod according to any one of claims 1 to 7.
9. The non-quenched and tempered steel wire rod according to claim 8, wherein the metallographic structure of the wire rod is bainite + ferrite, wherein the content of bainite is more than or equal to 85%, and the content of ferrite is less than 15%; the diameter of the wire rod is 8-18 mm, the tensile strength is 620-725 MPa, and the area shrinkage is 75-85%.
10. The non-quenched and tempered steel wire rod according to claim 8, wherein the wire rod can be drawn with a reduction of area of 20 to 65%, and the tensile strength of the wire rod after the drawing is 900 to 1505mpa, and the reduction of area is not less than 30%.
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Citations (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103695774A (en) * 2013-12-12 2014-04-02 山西新泰钢铁有限公司 Hot-rolled low-hardness steel containing titanium and boron for high-strength fastener and production method thereof
CN104593673A (en) * 2014-12-24 2015-05-06 张家港联峰钢铁研究所有限公司 Medium carbon non-annealed cold heading steel hot rolled wire rod and production method thereof
CN105945250A (en) * 2016-05-30 2016-09-21 内蒙古包钢钢联股份有限公司 Method for improving internal quality of high-alloy steel billet
CN111187992A (en) * 2020-02-26 2020-05-22 江苏省沙钢钢铁研究院有限公司 Production method of continuous casting billet of wire rod for cutting diamond wire
CN113025917A (en) * 2021-02-03 2021-06-25 江阴兴澄合金材料有限公司 Wire rod for low-strength high-plasticity annealing-free cold forging steel and manufacturing method thereof
CN113118405A (en) * 2021-03-10 2021-07-16 首钢集团有限公司 Small square billet continuous casting method of antimony-containing weather-resistant bolt steel
CN114318149A (en) * 2021-12-28 2022-04-12 张家港荣盛特钢有限公司 Grade 102 steel cord, grade 102 cord steel wire rod and production method thereof
CN115055654A (en) * 2022-08-16 2022-09-16 江苏省沙钢钢铁研究院有限公司 High-carbon steel wire rod and production method thereof
CN116121511A (en) * 2022-12-20 2023-05-16 青岛特殊钢铁有限公司 Production method for improving structural performance uniformity of SCM435 cold heading steel wire rod
CN116334498A (en) * 2023-05-29 2023-06-27 张家港荣盛特钢有限公司 Wire rod for steel strand and preparation method thereof
CN117089772A (en) * 2023-10-20 2023-11-21 江苏省沙钢钢铁研究院有限公司 High-quality sulfur-containing cold heading steel wire rod and preparation method thereof

Patent Citations (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103695774A (en) * 2013-12-12 2014-04-02 山西新泰钢铁有限公司 Hot-rolled low-hardness steel containing titanium and boron for high-strength fastener and production method thereof
CN104593673A (en) * 2014-12-24 2015-05-06 张家港联峰钢铁研究所有限公司 Medium carbon non-annealed cold heading steel hot rolled wire rod and production method thereof
CN105945250A (en) * 2016-05-30 2016-09-21 内蒙古包钢钢联股份有限公司 Method for improving internal quality of high-alloy steel billet
CN111187992A (en) * 2020-02-26 2020-05-22 江苏省沙钢钢铁研究院有限公司 Production method of continuous casting billet of wire rod for cutting diamond wire
CN113025917A (en) * 2021-02-03 2021-06-25 江阴兴澄合金材料有限公司 Wire rod for low-strength high-plasticity annealing-free cold forging steel and manufacturing method thereof
CN113118405A (en) * 2021-03-10 2021-07-16 首钢集团有限公司 Small square billet continuous casting method of antimony-containing weather-resistant bolt steel
CN114318149A (en) * 2021-12-28 2022-04-12 张家港荣盛特钢有限公司 Grade 102 steel cord, grade 102 cord steel wire rod and production method thereof
CN115055654A (en) * 2022-08-16 2022-09-16 江苏省沙钢钢铁研究院有限公司 High-carbon steel wire rod and production method thereof
CN116121511A (en) * 2022-12-20 2023-05-16 青岛特殊钢铁有限公司 Production method for improving structural performance uniformity of SCM435 cold heading steel wire rod
CN116334498A (en) * 2023-05-29 2023-06-27 张家港荣盛特钢有限公司 Wire rod for steel strand and preparation method thereof
CN117089772A (en) * 2023-10-20 2023-11-21 江苏省沙钢钢铁研究院有限公司 High-quality sulfur-containing cold heading steel wire rod and preparation method thereof

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