CN112267069B - Wire rod for 2100MPa grade galvanized steel wire and manufacturing method thereof - Google Patents
Wire rod for 2100MPa grade galvanized steel wire and manufacturing method thereof Download PDFInfo
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- 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
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/46—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting
- B21B1/463—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting in a continuous process, i.e. the cast not being cut before rolling
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B45/00—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
- B21B45/004—Heating the product
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/34—Methods of heating
- C21D1/44—Methods of heating in heat-treatment baths
- C21D1/46—Salt baths
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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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
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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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
- C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
- C22C33/06—Making ferrous alloys by melting using master alloys
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- 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
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- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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Abstract
The invention discloses a wire rod for a 2100MPa grade galvanized steel wire and a manufacturing method thereof. The manufacturing method comprises the following steps: 1) smelting molten steel according to the following chemical component design scheme, wherein the chemical components are calculated in percentage by mass: 0.96-0.98% of C, 1.00-1.09% of Si, 0.40-0.49% of Mn, 0.20-0.29% of Cr, 0.01-0.10% of Cu, 0.01-0.10% of Ni, 0.0005-0.0015% of B, and the balance of iron and inevitable impurities; 2) continuously casting the obtained molten steel into a blank; in the continuous casting process, the casting is started with the superheat degree of less than or equal to 20 ℃, and the reduction is controlled to be more than or equal to 25 mm; 3) cogging the continuous casting blank obtained in the step 2) to obtain an intermediate blank, and grinding the intermediate blank by using 16-mesh and 24-mesh grinding wheels in sequence, wherein the grinding depth of a single surface is more than or equal to 1.2mm, and the grinding depth of a corner part is not less than 2.0 mm; 4) and (3) hot rolling the intermediate blank polished in the step 3) into a wire rod through a high-speed wire rolling process, and then sequentially carrying out stelmor cooling and salt bath cooling and then carrying out coil collection to obtain the wire rod with high purity, uniform structure and high strength, and the wire rod is suitable for producing high-torsion galvanized steel wires with the diameter of 5-7 mm and the tensile strength of more than or equal to 2100 MPa.
Description
Technical Field
The invention belongs to the technical field of material preparation, and relates to a manufacturing method of a wire rod for a 2100 MPa-grade galvanized steel wire and the wire rod prepared by the manufacturing method.
Background
In recent years, the construction of large-span bridges in China has made great progress, and the application of a batch of symbolic engineering lays and consolidates the world leading position of China in the field. In the development process of world large-span bridges, materials always play an important role, and China is no exception. The galvanized steel wire of the bridge cable is a core material of a modern large-span bridge, and the grade and the quality of the galvanized steel wire have important influence on the level of a main span of the bridge.
At present, zinc-plated steel wires of 1960MPa class and 2000MPa class have been used in the major projects of Sisi hong bridge, Husutong bridge, etc., with satisfactory results. The built large-span bridge has already put higher requirements on galvanized steel wires, such as 7mm-2100MPa level proposed by the Heitai bridge.
The 2100MPa bridge cable galvanized steel wire has very high requirements on the wire rod, the wire rod is required to ensure high strength, and meanwhile, the wire rod has excellent characteristics of high purity, high uniformity, high surface quality and the like, and the conventional product cannot meet the requirements.
The prior art mainly improves the initial strength of a wire rod in an alloying mode so as to improve the strength of a galvanized steel wire, but the alloying mode can cause the reduction of the torsion property of the steel wire. Therefore, the patent provides a mode that microalloying combines the wire rod thermal treatment to produce high strength high plasticity wire rod, has solved among the prior art torsion problem of ultrahigh strength bridge cable galvanized steel wire.
Disclosure of Invention
The invention aims to provide a wire rod manufacturing method and a wire rod manufactured by the manufacturing method, wherein the wire rod has the advantages of ultrahigh strength, super uniformity and super cleanliness, and is suitable for manufacturing a high-torsion galvanized steel wire with a finished product diameter of 5-7 mm, a tensile strength of more than or equal to 2100MPa and a torsion coil number of more than or equal to 18 circles.
In order to achieve the above object, one embodiment of the present invention provides a method for manufacturing a wire rod for a 2100MPa grade galvanized steel wire, comprising the steps of:
1) smelting molten steel according to the following chemical component design scheme, wherein the chemical component design scheme comprises the following components in percentage by mass: 0.96-0.98% of C, 1.00-1.09% of Si, 0.40-0.49% of Mn, 0.20-0.29% of Cr, 0.01-0.10% of Cu, 0.01-0.10% of Ni, 0.0005-0.0015% of B, and the balance of iron and inevitable impurities;
2) continuously casting the molten steel obtained in the step 1) into a blank; in the continuous casting process, the casting is started with the superheat degree of less than or equal to 20 ℃, and the reduction is controlled to be more than or equal to 25 mm;
3) cogging the continuous casting blank obtained in the step 2) to obtain an intermediate blank, and grinding the intermediate blank by using 16-mesh and 24-mesh grinding wheels in sequence, wherein the grinding depth of a single surface is more than or equal to 1.2mm, and the grinding depth of a corner part is not less than 2.0 mm;
4) hot rolling the intermediate blank polished in the step 3) into a wire rod through a high-speed wire rolling process, then performing stelmor cooling and coil collection, and then performing salt bath cooling and coil collection again to obtain a finished wire rod product; during the salt bath cooling process, the wire rod is paid off and then subjected to off-line heat treatment and salt bath in sequence, the heating furnace keeps a nitrogen atmosphere and has the temperature of 950-1000 ℃, and the salt bath temperature is 530-560 ℃.
Preferably, the intermediate billet is hot-rolled into a wire rod with the diameter of 11-15 mm through a high-speed wire rolling process.
Preferably, the molten steel obtained in the step 1) is continuously cast into a continuous casting slab with the cross-sectional dimension of 300mm × 360mm to 300mm × 400 mm.
Preferably, in the stelmor cooling process of step 4), the cooling rate before austenite transformation is controlled to be more than 8K/s, and then coiling is carried out; in the salt bath cooling procedure, the wire rod is paid off and then is subjected to off-line heat treatment and salt bath in sequence, the heating furnace keeps a nitrogen atmosphere and has the temperature of 950-1000 ℃, and the salt bath temperature is 530-560 ℃.
Preferably, in the step 1), molten steel according with the chemical composition design scheme is prepared by molten iron desulphurization, converter smelting, LF refining and vacuum smelting in sequence; wherein the content of the first and second substances,
in the molten iron desulphurization procedure, the S content in the desulfurized molten iron is controlled to be less than 0.005 percent by mass;
in the converter smelting process, oxygen blowing smelting is carried out, the tapping temperature is controlled to be 1580-1620 ℃, the mass percent of C is 0.05-0.30%, and the mass percent of P is less than or equal to 90 ppm;
in the LF refining process, slagging is controlled to enable the binary alkalinity of the produced slag to be 2.3-2.8.
Preferably, in the continuous casting process of the step 2), the constant drawing speed of 0.58m/min is kept, the secondary cooling area is cooled by adopting gas mist, and the specific water amount is controlled to be less than 0.25L/kg.
Preferably, in the molten iron desulphurization procedure, a KR desulphurization technology is adopted, and a desulfurizer CaO is added to remove sulfur in molten iron, so that the S content in the desulfurized molten iron is controlled to be less than 0.005 percent in mass percentage.
Preferably, in the LF refining process, SiCa wires are fed in the later stage of refining, argon gas is used for soft stirring for 15min after wire feeding, and a heat insulating agent is added.
Preferably, in the converter smelting process, the stirring pressure of argon is 1MPa, and a deoxidizer is added when the steel is tapped to 1/3, so that the steel is tapped to avoid slag falling.
Preferably, in the vacuum smelting process, a VD furnace is used for vacuum treatment, and the vacuum degree is less than or equal to 1 mbar.
Preferably, in the step 3), the continuous casting slab obtained in the step 2) is heated in a heating furnace, the air-fuel ratio of a heating section is maintained below 0.75, the air-fuel ratio of a soaking section is maintained below 0.65, the heating temperature is 1180-1230 ℃, and rough rolling and cogging are carried out at the rolling temperature of 1100 ℃ to obtain an intermediate billet with the cross section size of 140mm multiplied by 140 mm.
Preferably, in the high-speed wire rolling procedure in the step 4), the temperature of a soaking section before hot rolling is 1160-1200 ℃, the air-fuel ratio of the soaking section is less than 0.65, the initial rolling temperature is 1015-1045 ℃, the finish rolling temperature is 950-980 ℃, and the spinning temperature is 840-860 ℃.
In order to achieve the purpose, one embodiment of the invention provides a wire rod for 2500 MPa-grade steel strands, which is prepared by adopting the manufacturing method.
Preferably, the tensile strength Rm of the wire rod is 1580-1630 MPa, the reduction of area Z is more than or equal to 30%, and the elongation A after fracture is more than or equal to 11%.
Preferably, the co-winding strength fluctuation of the wire rod is within +/-12 MPa.
Preferably, the surface crack depth of the wire rod is less than or equal to 40 mu m, and the depth of the decarburized layer is less than or equal to 60 mu m.
Preferably, the grades of the inclusions in the A class, the B class, the C class and the D class of the wire rod are all less than or equal to 1.0 grade, the grades of the reticular cementite are less than or equal to 1.0 grade, and the grades of the martensite are less than or equal to 1.5 grade.
Preferably, the wire rod can be used for preparing a finished galvanized steel wire with the diameter of 5-7 mm, the tensile strength of more than or equal to 2100MPa and the number of torsion turns of more than or equal to 18 turns.
Preferably, the wire rod can be used for preparing a finished galvanized steel wire with the diameter of 5mm, the tensile strength of more than or equal to 2100MPa and the number of turns of torsion of more than or equal to 18 turns.
Compared with the prior art, the invention has the beneficial effects that:
(1) the carbon content is increased, so that the cementite proportion in the wire rod is increased, the strength of the wire rod is further improved, and the plasticity of the wire rod is reduced; compared with the alloying mode in the prior art, the invention improves the plasticity by improving the uniformity of the material mainly through process control;
(2) on one hand, the Si element is added to improve the strength of the wire rod by utilizing the solid solution strengthening effect; on the other hand, the steel wire is used for reducing the strength loss in the subsequent steel wire galvanizing process;
(3) by adding a proper amount of Cr, the pearlite lamellar spacing is reduced, and the strength of the wire rod is improved. Meanwhile, Cr is a carbide forming element and can inhibit the spheroidization of subsequent steel wire cementite lamella, the spheroidization effect of the steel wire needs to be utilized, and the Cr content must be strictly controlled;
(4) the solidification segregation is further reduced and the material uniformity is improved through the cogging process and the salt bath cooling process, so that the strength and the plasticity of the wire rod are improved;
(5) by controlling the superheat degree and the reduction in the continuous casting process, the strength can be improved by the design of chemical components, the macrosegregation is greatly reduced, and the uniformity of the structure is ensured;
(6) through the control of the coping process, the cost is saved and reduced, and meanwhile, the surface decarburization generated in the heating process of the cogging process is eliminated, and the surface cracks of the continuous casting billet are reduced;
(7) the wire rod has the advantages of high purity, uniform structure, good surface quality, high strength and good plasticity, the diameter is 11-15 mm, the tensile strength Rm is 1580-1630 MPa, the reduction of area Z is more than or equal to 30%, the elongation after fracture A is more than or equal to 11%, the strength fluctuation of the same coil is within +/-12 MPa, the depth of surface cracks is less than or equal to 40 microns, the depth of a decarburized layer is less than or equal to 60 microns, the grades of inclusions of A, B, C and D are less than or equal to 1.0 grade, the grades of reticular cementite are less than or equal to 1.0 grade, and the martensite is less than or equal to 1.5 grade.
(8) After wire drawing, hot galvanizing and stabilizing treatment are carried out on the obtained wire rod, a finished product of the high-torsion galvanized steel wire with the diameter of 5-7 mm, the tensile strength of more than or equal to 2100MPa and the number of torsion turns of more than or equal to 18 turns can be prepared, and the method is particularly suitable for large-span bridge cables.
Detailed Description
The technical solutions of the present invention will be further described with reference to specific embodiments, and the technical contents described below are only exemplary embodiments of the present invention and are not intended to limit the scope of the present invention, which is defined by the appended claims.
The embodiment provides a manufacturing method of a wire rod and the wire rod prepared by the manufacturing method, the wire rod has the advantages of ultrahigh strength, super uniformity, super purity and good plasticity, and is suitable for preparing a high-torsion galvanized steel wire with a finished product diameter of 5-7 mm, a tensile strength of more than or equal to 2100MPa and a torsion coil number of more than or equal to 18 coils. The manufacturing method comprises the working procedures of molten iron desulfurization, converter smelting, LF refining, vacuum smelting, continuous casting, cogging, coping, high-speed wire rolling, stelmor cooling, salt bath cooling and the like.
The wire rod comprises the following chemical components in percentage by mass: 0.96-0.98% of C, 1.00-1.09% of Si, 0.40-0.49% of Mn, 0.20-0.29% of Cr, 0.01-0.10% of Cu, 0.01-0.10% of Ni, 0.0005-0.0015% of B, and the balance of iron and inevitable impurities.
Preferred embodiments of the respective steps of the manufacturing method will be described below.
(1) Molten iron desulphurization
And (3) adopting a KR desulfurization technology, adding a desulfurizer CaO to remove sulfur in the molten iron so as to control the S content in the desulfurized molten iron to be less than 0.005 percent in mass percentage.
(2) Smelting in a converter
Transferring the desulfurized molten iron obtained in the molten iron desulfurization procedure into a converter, adding scrap steel for smelting, and performing oxygen blowing smelting, wherein the tapping temperature is controlled to be 1580-1620 ℃, the mass percent of C is 0.05-0.30%, and the mass percent of P is less than or equal to 90 ppm; argon stirring pressure is 1MPa, a deoxidizer is added when the steel is tapped to 1/3, and slag is prevented from being discharged when the steel is tapped.
(3) LF refining
Transferring the steel smelted by the converter into an LF furnace for refining, heating, raising the temperature, carrying out alloying treatment according to the chemical composition design scheme, and controlling slagging in the refining process to ensure that the binary alkalinity of the slag is 2.3-2.8; SiCa wire is fed in the later period of refining, argon gas is used for soft stirring for 15min after wire feeding, and carbonized rice husk and other heat insulating agents are added.
(4) Vacuum smelting
And putting the molten steel obtained by LF refining into a VD furnace for vacuum treatment, wherein the vacuum degree is less than or equal to 1mbar, and the vacuum treatment time is not less than 30min, so as to finally prepare the molten steel meeting the chemical composition design scheme.
(5) Continuous casting
Continuously casting the molten steel obtained in the vacuum smelting into a continuous casting billet with the cross section size of 300mm multiplied by 360 mm-300 mm multiplied by 400mm, preferably a continuous casting billet with the cross section size of 300mm multiplied by 390 mm; in the continuous casting process, the casting is started with the superheat degree less than or equal to 20 ℃, the constant drawing speed of 0.58m/min is kept, the secondary cooling zone adopts gas mist cooling, the specific water amount is controlled to be less than 0.25L/kg, and the reduction amount is controlled to be more than or equal to 25 mm.
(6) Cogging and cogging
Heating the continuous casting billet obtained in the continuous casting process in a heating furnace, maintaining the air-fuel ratio of a heating section below 0.75, maintaining the air-fuel ratio of a soaking section below 0.65, heating at 1180-1230 ℃, and performing rough rolling and cogging at the cogging temperature of 1100 ℃ to obtain an intermediate billet with the cross section size of 140mm multiplied by 140 mm.
(7) Grinding
Grinding the intermediate blank prepared in the blank opening procedure by using 16-mesh and 24-mesh grinding wheels in sequence, wherein the grinding depth of a single surface is more than or equal to 1.2mm, and the grinding depth of corners is not less than 2.0 mm.
(8) High speed wire rolling
Hot rolling the intermediate blank after the coping process into a wire rod with the diameter of 11-15 mm through a high-speed wire rolling process; the temperature of a soaking section before hot rolling is 1160-1200 ℃, the air-fuel ratio of the soaking section is less than 0.65, the initial rolling temperature is 1015-1045 ℃, the finish rolling temperature is 950-980 ℃, and the spinning temperature is 840-860 ℃.
(9) Stelmor cooling
The wire rod produced in the high-speed wire rolling step is cooled on a stelmor cooling line, and the cooling rate before austenite transformation (corresponding to a temperature of about 630 ℃ or higher) is controlled to 8K/s or higher, and then the wire rod is coiled.
(10) Salt bath cooling
Paying off the wire rod obtained by coiling in the stelmor cooling procedure, and then sequentially performing off-line heat treatment and salt bath, wherein the paid-off wire rod enters a heating furnace for temperature control heating, the heating furnace keeps a nitrogen atmosphere and the temperature is 950-1000 ℃, the heating time is more than 10-15 min, the salt bath temperature is controlled to be 530-560 ℃, and the salt bath time is 3-6 min; and (4) performing the rolling again after the salt bath process, and finally obtaining a finished product of the wire rod.
The wire rod provided by the embodiment of the invention is prepared by the manufacturing method, has the advantages of high purity, uniform tissue, good surface quality, high strength and good plasticity, has the diameter of 11-15 mm, the tensile strength Rm of 1580-1630 MPa, the reduction of area Z of more than or equal to 30%, the elongation after fracture A of more than or equal to 11%, the fluctuation of strength in the same roll of +/-12 MPa, the depth of surface cracks of less than or equal to 40 mu m, the depth of a decarburized layer of less than or equal to 60 mu m, the grades of inclusions of A, B, C and D are all less than or equal to 1.0 grade, the grades of reticular cementite are less than or equal to 1.0 grade, and the grades of martensite are less than or equal to 1.5 grade.
In general, compared with the prior art, the invention has the following beneficial effects: through the design of chemical components and the improvement of the process technology matched with the production method, the size and the type of impurities are strictly controlled, the high purity and the uniform structure are ensured, and the tensile strength and the drawing performance of the wire rod are improved; after wire rods are subjected to wire drawing, hot galvanizing and stabilizing treatment, the finished high-torsion galvanized steel wire with the diameter of 5-7 mm, the tensile strength of more than or equal to 2100MPa and the number of torsion turns of more than or equal to 18 turns can be prepared, and the method is particularly suitable for large-span bridge cables.
In order to make the objects, technical solutions and advantages of an embodiment of the present invention more clear, the embodiment will be further described with reference to examples 1 to 4 according to an embodiment of the present invention and comparative examples 1 to 3 not according to an embodiment of the present invention. It is clear that the embodiments 1 to 4 described are some, but not all, embodiments of the present invention.
Specifically, examples 1 to 4 and comparative examples 1 to 5 each provide a wire rod, each of which has chemical components in mass percent as shown in table 1.
[ Table 1]
| C | Si | Mn | Cr | Cu | Ni | B | |
| Example 1 | 0.96 | 1.01 | 0.40 | 0.20 | 0.02 | 0.03 | 0.0005 |
| Example 2 | 0.97 | 1.05 | 0.45 | 0.25 | 0.03 | 0.03 | 0.0010 |
| Example 3 | 0.98 | 1.07 | 0.49 | 0.29 | 0.05 | 0.03 | 0.0015 |
| Example 4 | 0.96 | 1.01 | 0.49 | 0.22 | 0.09 | 0.10 | 0.0012 |
| Comparative example 1 | 0.96 | 1.25 | 0.41 | 0.20 | 0.03 | 0.03 | 0.0012 |
| Comparative example 2 | 0.97 | 1.08 | 0.45 | 0.35 | 0.04 | 0.03 | 0.0020 |
| Comparative example 3 | 0.96 | 1.07 | 0.48 | 0.25 | 0.05 | 0.08 | 0.0009 |
| Comparative example 4 | 0.98 | 1.05 | 0.45 | 0.25 | 0.05 | 0.07 | 0.0010 |
| Comparative example 5 | 0.96 | 1.06 | 0.49 | 0.25 | 0.06 | 0.06 | 0.0009 |
As can be seen from table 1, examples 1 to 4 all conform to the chemical composition design scheme in an embodiment of the present invention, that is, the chemical compositions in mass percent are: 0.96-0.98% of C, 1.00-1.09% of Si, 0.40-0.49% of Mn, 0.20-0.29% of Cr, 0.01-0.10% of Cu, 0.01-0.10% of Ni, 0.0005-0.0015% of B, and the balance of iron and inevitable impurities. The comparative examples 1-2 do not accord with the chemical composition design scheme, and the comparative examples 3-5 compound the chemical composition design scheme, but the production process is different.
Specifically, the manufacturing methods of examples 1 to 4 and comparative examples 1 to 5 were as follows:
(1) molten iron desulphurization
In examples 1 to 4 and comparative examples 1 to 5, KR desulfurization technology was used, and a desulfurizing agent CaO was added to desulfurize molten iron so as to control the S content in the desulfurized molten iron to be less than 0.005% by mass.
(2) Smelting in a converter
In examples 1 to 4 and comparative examples 1 to 5, 115t of desulfurized molten iron obtained in the molten iron desulfurization procedure was transferred to a 120t converter, and high-quality scrap steel was added for smelting, and oxygen blowing smelting was performed, with the tapping temperature controlled at 1600 ℃, the mass percentages of C being 0.05 to 0.30%, and P being less than or equal to 90 ppm; argon stirring pressure is 1MPa, a deoxidizer is added when the steel is tapped to 1/3, and slag is prevented from being discharged when the steel is tapped.
(3) LF refining
In the examples 1 to 4 and the comparative examples 1 to 5, the steel tapping smelted by the converter is transferred into an LF furnace for refining, the heating and the temperature rise are carried out, alloying treatment is carried out according to the chemical composition design scheme, and slagging is controlled in the refining process so that the binary alkalinity of the slag is 2.3 to 2.8; SiCa wire is fed in the later period of refining, argon gas is used for soft stirring for 15min after wire feeding, and carbonized rice husk and other heat insulating agents are added.
(4) Vacuum smelting
In the examples 1 to 4 and the comparative examples 1 to 5, the molten steel obtained by LF refining is put into a VD furnace for vacuum treatment, the vacuum degree is less than or equal to 1mbar, the vacuum treatment time is not less than 30min, and the molten steel with the chemical components shown in the table 1 is finally obtained by smelting in the examples 1 to 4 and the comparative examples 1 to 5.
(5) Continuous casting
In examples 1 to 4, comparative examples 1 to 3 and comparative example 5, molten steel obtained in vacuum smelting was continuously cast into continuous casting slabs having cross-sectional dimensions of 300mm × 390 mm; in the continuous casting process, beginning to pour at the superheat degree of less than or equal to 20 ℃, keeping the constant drawing speed of 0.58m/min, cooling the secondary cooling zone by adopting gas mist, controlling the specific water amount to be less than 0.25L/kg, and controlling the reduction amount to be more than or equal to 25 mm;
in contrast, comparative example 4, the molten steel obtained in the vacuum smelting was continuously cast into a continuous casting slab having a cross-sectional size of 300mm × 390 mm; in the continuous casting process, the casting is started with the superheat degree less than or equal to 20 ℃, the constant drawing speed of 0.58m/min is kept, the secondary cooling zone adopts gas mist cooling, the specific water amount is controlled to be less than 0.25L/kg, and the reduction amount is controlled to be 18 mm.
(6) Cogging and cogging
In examples 1 to 4 and comparative examples 1 to 5, the continuous casting slabs obtained in the continuous casting process were heated in a heating furnace, the air-fuel ratio of the heating zone was maintained at 0.75, the air-fuel ratio of the soaking zone was maintained at 0.65, the heating temperature was 1180 to 1230 ℃, the total heating time was not less than 5 hours, and rough rolling and cogging were performed at a cogging temperature of 1100 ℃ to obtain intermediate slabs having a cross-sectional size of 140mm × 140 mm.
(7) Grinding
In the examples 1-4 and the comparative examples 1-4, the intermediate blanks prepared in the blank opening procedure are ground by using 16-mesh and 24-mesh grinding wheels, the grinding depth of a single surface is more than or equal to 1.2mm, and the grinding depth of corners is not less than 2.0 mm;
in contrast, in comparative example 5, the intermediate blank obtained in the blank opening process was polished with a 16-mesh grinding wheel, and the single-side polishing depth was about 1.0mm and the corner polishing depth was about 1.0 mm.
(8) High speed wire rolling
In each of examples 1 to 4 and comparative examples 1 to 5, the intermediate billet after the coping process was hot-rolled into a wire rod through a high-speed wire rolling process; the temperature of the soaking section before hot rolling is 1160-1200 ℃, the air-fuel ratio of the soaking section is less than 0.65, the initial rolling temperature is 1030 ℃, the finish rolling temperature is 950-980 ℃, the spinning temperature is 840-860 ℃, and the diameters (see the specification in the following table 3) of the wire rods in the examples 1-4 and the comparative examples 1-5 are 11mm, 13mm, 14mm, 13mm, 14mm, and 14mm, respectively.
(9) Stelmor cooling
In each of examples 1 to 4 and comparative examples 1 to 5, the wire rod obtained in the high-speed wire rolling process was cooled on a stelmor cooling line, and the cooling rate before austenite transformation (corresponding to a temperature of about 630 ℃ or higher) was controlled to 8K/s or more, and then the wire rod was collected.
(10) Salt bath cooling
In the embodiments 1-4 and the comparative examples 1-2 and the comparative examples 4-5, the wire rod obtained by coiling in the stelmor cooling process is paid off and then is subjected to off-line heat treatment and salt bath in sequence, wherein the paid off wire rod enters a heating furnace for temperature control heating, the heating furnace maintains a nitrogen atmosphere, the temperature is 950-1000 ℃, the heating time is 10-15 min or more, the salt bath temperature is 530-560 ℃, and the salt bath time is 3-6 min; performing the salt bath process and then performing the coiling again to finally prepare a finished product of the wire rod;
in the comparative example 3, the wire rod obtained by coiling in the stelmor cooling procedure is paid off and then is subjected to off-line heat treatment and salt bath in sequence, wherein the paid off wire rod enters a heating furnace for temperature control heating, the heating furnace keeps a nitrogen atmosphere and the temperature is 970-1030 ℃, the heating time is more than 8-12 min, the salt bath temperature is controlled to be 530-560 ℃, and the salt bath time is 2-4 min; and (4) performing the rolling again after the salt bath process, and finally obtaining a finished product of the wire rod.
That is, comparative example 3 is the same as examples 1 to 4 except that the salt bath cooling step is different from examples 1 to 4; comparative example 4 the same procedures as in examples 1 to 4 were carried out except that the continuous casting procedure was different from those in examples 1 to 4; comparative example 5 the same process as in examples 1 to 4 was carried out except that the thinning process was different from that of examples 1 to 4.
The grades of the type a, type B, type C and type D inclusions of the wire rods of examples 1 to 4 and comparative examples 1 to 5 were measured, respectively, and the results are shown in table 2.
[ Table 2]
| Class A, class C | Class B, class C | Class C, class C | Class D, class D | |
| Example 1 | 0.5 | 0.5 | 0.5 | 0 |
| Example 2 | 1.0 | 0.5 | 0.5 | 0.5 |
| Example 3 | 1.0 | 0.5 | 1.0 | 0.5 |
| Example 4 | 1.0 | 0.5 | 0.5 | 0 |
| Comparative example 1 | 0.5 | 0.5 | 0.5 | 0 |
| Comparative example 2 | 1.0 | 0.5 | 0.5 | 0.5 |
| Comparative example 3 | 1.0 | 0.5 | 0.5 | 0.5 |
| Comparative example 4 | 1.5 | 0.5 | 0.5 | 0 |
| Comparative example 5 | 0.5 | 0.5 | 0.5 | 0 |
The structure and mechanical properties of the wire rods of examples 1 to 4 and comparative examples 1 to 5 were respectively measured, and the results are shown in table 3, specifically including the diameter of the wire rod (i.e., the specification in table 3), tensile strength, average reduction of area (i.e., Z in table 3), average elongation after fracture (i.e., a in table 3), martensite grade, mesh cementite (i.e., mesh carbon in table 3) grade, surface crack depth, and decarburized layer depth.
[ Table 3]
Further, the wire rods of the examples 1 to 4 and the comparative examples 1 to 5 are respectively subjected to 9-pass drawing, then hot-dip galvanized aluminum is adopted by a double pot method, the temperature of hot galvanizing and hot-dip galvanized aluminum is 440-460 ℃, then stabilization is carried out at 380 ℃, and finally wire rewinding is carried out to obtain the finished hot-dip galvanized aluminum steel wire. The specifications and mechanical property indexes of the finished steel wires obtained by further preparing the wire rods in the examples 1-4 and the comparative examples 1-5 are shown in the table 4.
[ Table 4]
| Specification, mm | Tensile strength, MPa | Elongation percentage of% | Torsion, ring | Fatigue, second degree | |
| Example 1 | 5.1 | 2203 | 5.5 | 22-24 | 235 |
| Example 2 | 6.0 | 2185 | 5.2 | 23-24 | 240 |
| Example 3 | 7.0 | 2147 | 5.0 | 21-23 | 239 |
| Example 4 | 7.0 | 2212 | 4.9 | 21-24 | 246 |
| Comparative example 1 | 7.0 | 2135 | 5.2 | 13-22 | 170 |
| Comparative example 2 | 6.0 | 2201 | 5.1 | 3-8 | 220 |
| Comparative example 3 | 7.0 | 2145 | 5.0 | 8-22 | 235 |
| Comparative example 4 | 7.0 | 2150 | 4.5 | 4-7 | 190 |
| Comparative example 5 | 7.0 | 2145 | 5.0 | 4-12 | 180 |
As can be seen by combining tables 1 to 4:
the wire rod has the advantages of high purity, uniform structure, good surface quality, high strength and good plasticity, can be used for producing a finished product of a high-torsion galvanized steel wire with the diameter of 5-7 mm, the tensile strength of more than or equal to 2100MPa and the number of torsion turns of more than or equal to 18 turns, and has excellent mechanical properties;
in the comparative example 1, the depth of the decarburization layer of the wire rod cannot be controlled due to the over-high Si content, the depth of the decarburization layer of the wire rod reaches 125 mu m, and finally the fatigue performance of the hot-dip galvanized aluminum steel wire is lower than the requirement of 200 ten thousand times in the industry standard;
comparative example 2 because the Cr content is too high, the steel wire can not be spheroidized in the hot galvanizing process, and the torsion value of the final finished hot galvanized aluminum steel wire is poorer and can not meet the standard requirement of 14 times;
comparative example 3 because the linear velocity is fast, salt bath temperature control is low, cause the tensile strength of the same coil of wire rod to fluctuate greatly, and then cause the torsion performance of the steel wire to be unstable, can not all reach the standard requirement of 14 times;
comparative example 4 because of insufficient rolling reduction of the continuous casting billet, the surface shrinkage rate of the wire rod is low due to serious center segregation, wire breakage occurs in wire drawing, and the torsion and fatigue values are low;
in comparative example 5, the grinding amount of the surface and the corners of the blank is insufficient, so that the surface cracks and the decarburization and removal of the corners of the blank are not clean, and the torsion and fatigue values of the final steel wire are not satisfactory.
The detailed description set forth above is merely a specific description of possible embodiments of the present invention and is not intended to limit the scope of the invention, which is intended to include within the scope of the invention equivalent embodiments or modifications that do not depart from the technical spirit of the present invention.
Claims (12)
1. A manufacturing method of a wire rod for 2100MPa grade galvanized steel wires is characterized by comprising the following steps:
1) smelting molten steel according to the following chemical component design scheme, wherein the chemical component design scheme comprises the following components in percentage by mass: 0.96-0.98% of C, 1.00-1.09% of Si, 0.40-0.49% of Mn, 0.20-0.29% of Cr, 0.01-0.10% of Cu, 0.01-0.10% of Ni, 0.0005-0.0015% of B, and the balance of iron and inevitable impurities;
2) continuously casting the molten steel obtained in the step 1) into a blank; in the continuous casting process, the casting is started with the superheat degree of less than or equal to 20 ℃, and the reduction is controlled to be more than or equal to 25 mm;
3) cogging the continuous casting blank obtained in the step 2) to obtain an intermediate blank, and grinding the intermediate blank by using 16-mesh and 24-mesh grinding wheels in sequence, wherein the grinding depth of a single surface is more than or equal to 1.2mm, and the grinding depth of a corner part is not less than 2.0 mm;
4) hot rolling the polished intermediate blank in the step 3) into a wire rod with the diameter of 11-15 mm through a high speed wire rolling process, wherein the temperature of a soaking section before hot rolling is 1160-1200 ℃, the initial rolling temperature is 1015-1045 ℃, the finish rolling temperature is 950-980 ℃, and the spinning temperature is 840-860 ℃; then, performing stelmor cooling on the wire rod prepared in the high-speed wire rolling procedure, then performing coil collection, cooling by a salt bath, and then performing coil collection again to obtain a wire rod finished product with the tensile strength Rm of 1580-1630 MPa, the same coil strength fluctuation within +/-12 MPa, the reduction of area Z of more than or equal to 30 percent and the elongation after fracture A of more than or equal to 11 percent; during the salt bath cooling process, the wire rod is paid off and then subjected to off-line heat treatment and salt bath in sequence, the heating furnace keeps a nitrogen atmosphere and has the temperature of 950-1000 ℃, and the salt bath temperature is 530-560 ℃.
2. The method of manufacturing a wire rod for a 2100MPa grade galvanized steel wire according to claim 1, characterized in that a cooling rate before austenite transformation is controlled to be 8K/s or more in Steyr cooling.
3. The method for manufacturing the wire rod for the 2100MPa grade galvanized steel wire according to claim 1, characterized in that the molten steel obtained in the step 1) is continuously cast into a continuous casting billet with the cross-sectional dimension of 300mm x 360mm to 300mm x 400 mm.
4. The method for manufacturing the wire rod for the 2100 MPa-grade galvanized steel wire according to claim 1, characterized in that in the step 3), the continuous casting billet obtained in the step 2) is heated in a heating furnace, the air-fuel ratio of a heating section is maintained below 0.75, the air-fuel ratio of a soaking section is maintained below 0.65, the heating temperature is 1180-1230 ℃, and rough rolling cogging is performed at a cogging temperature of 1100 ℃ to obtain an intermediate billet with the cross section size of 140mm x 140 mm.
5. The method for manufacturing the wire rod for the 2100 MPa-grade galvanized steel wire according to claim 1, wherein in the step 1), molten steel conforming to the chemical composition design scheme is manufactured by molten iron desulphurization, converter smelting, LF refining and vacuum smelting in sequence; wherein the content of the first and second substances,
in the molten iron desulphurization procedure, the S content in the desulfurized molten iron is controlled to be less than 0.005 percent by mass;
in the converter smelting process, oxygen blowing smelting is carried out, the tapping temperature is controlled to be 1580-1620 ℃, the mass percent of C is 0.05-0.30%, and the mass percent of P is less than or equal to 90 ppm;
in the LF refining process, slagging is controlled to enable the binary alkalinity of the produced slag to be 2.3-2.8.
6. A wire rod for a 2100MPa grade galvanized steel wire, characterized by being produced by the production method according to any one of claims 1 to 5.
7. The wire rod for the 2100 MPa-grade galvanized steel wire according to claim 6, characterized in that the tensile strength Rm of the wire rod is 1580-1630 MPa, the reduction of area Z is not less than 30%, and the elongation after fracture A is not less than 11%.
8. The 2100MPa grade galvanized steel wire rod according to claim 6, characterized in that the same coil strength fluctuation of the rod is within ± 12 MPa.
9. The wire rod for the 2100MPa grade galvanized steel wire according to claim 6, characterized in that the surface crack depth of the wire rod is less than or equal to 40 μm, and the decarburized layer depth is less than or equal to 60 μm.
10. The wire rod for the 2100MPa grade galvanized steel wire according to claim 6, characterized in that the grades of the A-type, B-type, C-type and D-type inclusions of the wire rod are all less than or equal to 1.0 grade, the grades of the reticular cementite are less than or equal to 1.0 grade, and the grades of the martensite are less than or equal to 1.5 grade.
11. The wire rod for the 2100MPa grade galvanized steel wire according to claim 6, characterized in that the wire rod can be used for preparing a finished product of the galvanized steel wire with the diameter of 5-7 mm, the tensile strength of more than or equal to 2100MPa and the number of turns of torsion of more than or equal to 18 turns.
12. The wire rod for the 2100MPa grade galvanized steel wire according to claim 11, characterized in that the wire rod can be used for preparing a finished galvanized steel wire with a diameter of 5mm, a tensile strength of more than or equal to 2100MPa and a number of turns of torsion of more than or equal to 18 turns.
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| CN114032372B (en) * | 2021-11-25 | 2023-02-17 | 张家港荣盛特钢有限公司 | Wire rod, heat treatment method and production method thereof and galvanized steel wire |
| CN114985468A (en) * | 2022-06-21 | 2022-09-02 | 湖南华菱湘潭钢铁有限公司 | Method for controlling depth of decarburized layer of hot-rolled cold-heading steel coil |
| CN114807728B (en) * | 2022-06-30 | 2022-11-18 | 江苏省沙钢钢铁研究院有限公司 | 2100MPa grade spring steel wire and production method thereof |
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