CN114807728B - 2100MPa grade spring steel wire and production method thereof - Google Patents

2100MPa grade spring steel wire and production method thereof Download PDF

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CN114807728B
CN114807728B CN202210754602.0A CN202210754602A CN114807728B CN 114807728 B CN114807728 B CN 114807728B CN 202210754602 A CN202210754602 A CN 202210754602A CN 114807728 B CN114807728 B CN 114807728B
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steel wire
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CN114807728A (en
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麻晗
陈焕德
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Institute Of Research Of Iron & Steel shagang jiangsu Province
Jiangsu Shagang Group Co Ltd
Zhangjiagang Rongsheng Special Steel Co Ltd
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Institute Of Research Of Iron & Steel shagang jiangsu Province
Jiangsu Shagang Group Co Ltd
Zhangjiagang Rongsheng Special Steel Co Ltd
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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
    • 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
    • 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
    • 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
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

The invention discloses a 2100MPa grade spring steel wire and a production method thereof. Chemical components of the steel wire: 0.53 to 0.57 percent of C, 1.61 to 1.81 percent of Si, 0.7 to 0.8 percent of Mn, 0.81 to 0.91 percent of Cr, 0.11 to 0.19 percent of V, 0.02 to 0.04 percent of Nb, 0.01 to 0.09 percent of Ni, 0.01 to 0.10 percent of Mo, less than or equal to 0.002 percent of O, less than or equal to 0.003 percent of N, less than or equal to 0.002 percent of Al, less than or equal to 0.001 percent of Ti, less than or equal to 0.005 percent of Sn, less than or equal to 0.01 percent of S, less than or equal to 0.01 percent of P, less than or equal to 0.0002 percent of H, and the balance of Fe and impurities, { [ V ] + [ Nb ] }/{ [ C ] + [ N ] } 0.23 to 0.4. The 2100MPa grade spring steel wire can be prepared, the reduction of area is more than or equal to 48 percent, and the service requirement of a large-load automobile suspension system can be met.

Description

2100MPa grade spring steel wire and production method thereof
Technical Field
The invention belongs to the technical field of steel production, and relates to a production method of a 2000 MPa-level spring steel wire and a 2100 MPa-level spring steel wire.
Background
The spring is widely applied to the fields of automobiles, machinery, railways and the like as a safety bearing part, and often bears high-cycle alternating load in the service process. Under the large background of energy conservation, emission reduction and green development, the new energy automobile enters a rapid development stage, and the market share of the electric automobile is continuously improved; compared with the traditional fuel vehicle, the weight of the electric vehicle is greatly improved, so that higher requirements are provided for the bearing capacity of a suspension system, and therefore springs with higher strength and better plasticity need to be developed to meet the service requirements of the springs in the suspension system of the electric vehicle.
At present, the mainstream products of the domestic automobile suspension springs are springs with tensile strength of 1900 MPa and 2000MPa, and cannot meet the service requirements of a suspension system of an electric automobile with larger weight. However, the existing production technology can improve the tensile strength of the spring and simultaneously cause the plasticity of the spring to be reduced, and the service requirement under large load cannot be met.
Disclosure of Invention
The invention aims to provide a 2100MPa grade spring steel wire and a production method thereof, and also relates to a 2100MPa grade spring steel wire.
In order to achieve the above object, one embodiment of the present invention provides a production method of a 2100MPa grade spring steel wire, which is characterized in that the spring steel wire comprises the following chemical components by mass percent: 0.53 to 0.57 percent of C, 1.61 to 1.81 percent of Si, 0.7 to 0.8 percent of Mn, 0.81 to 0.91 percent of Cr, 0.11 to 0.19 percent of V, 0.02 to 0.04 percent of Nb, 0.01 to 0.09 percent of Ni, 0.01 to 0.10 percent of Mo, less than or equal to 0.002 percent of O, less than or equal to 0.003 percent of N, less than or equal to 0.002 percent of Al, less than or equal to 0.001 percent of Ti, less than or equal to 0.005 percent of Sn, less than or equal to 0.01 percent of S, less than or equal to 0.01 percent of P, less than or equal to 0.0002 percent of H, and the balance of Fe and inevitable impurities, wherein { [ V ] + [ Nb ] }/{ [ C ] + [ N ] } =0.23 to 0.4; the production method comprises the working procedures of molten iron pre-desulfurization, converter smelting, LF refining, vacuum refining, bloom continuous casting, cogging, coping, high-speed wire rolling, controlled cooling, acid pickling, drawing and heat treatment which are sequentially carried out; wherein:
in the LF refining process, the alkalinity of refining slag is 1.3 to 1.6;
in the continuous casting process of the bloom, electromagnetic tail end stirring and continuous casting under high pressure are adopted, and the total pressure reduction is 13-19mm;
in the coping process, the surface of the small square billet obtained in the blank opening process is grinded, and the surface roughness Ra of the grinded small square billet is less than or equal to 0.1 mu m;
in the high-speed wire rolling process, the billet is rolled into a wire rod, the rolling temperature is 950 to 1050 ℃, and the spinning temperature is 850 to 900 ℃;
in the controlled cooling process, the cooling speed before pearlite transformation is 2.1 to 3.0 ℃/s, the pearlite transformation starting temperature is 650 to 750 ℃, the cooling speed in the pearlite transformation stage is less than or equal to 1 ℃/s, and the interlayer spacing of pearlite pieces is controlled to be less than or equal to 170nm;
in the heat treatment process, the steel wire obtained in the drawing process is sequentially quenched and tempered on a production line configured with online induction heating, wherein the quenching temperature is Ar < 3+ > 20 ℃ -Ar < 3+ >50 ℃, ar < 3 > is the austenitizing temperature of the steel wire, and the tempering temperature is 395-415 ℃.
Preferably, in the molten iron pre-desulfurization process, the molten iron is desulfurized until S in the molten iron is less than or equal to 0.002%;
in the converter smelting process, smelting a smelting raw material consisting of scrap steel and pre-desulfurized molten iron in a converter, wherein the molten iron accounts for more than or equal to 85% of the smelting raw material by weight;
in the LF refining process, low-aluminum low-titanium alloy is adopted to carry out alloying treatment on molten steel;
in the vacuum refining process, after the refining furnace is subjected to vacuum treatment, the molten steel is subjected to soft stirring, and the soft stirring time is more than or equal to 30min.
Preferably, in the cogging procedure, the continuous casting blank is heated in a heating furnace and then is subjected to continuous rolling for 9 times, and is cogging into a small square blank with the cross section of 150mm multiplied by 150mm, the heating temperature is 1150-1200 ℃, and the furnace time is less than or equal to 240min.
Preferably, in the grinding process, a grinder is adopted to perform coarse grinding and fine grinding on the surface of the small square billet in sequence, and the grinding depth of a single side is more than or equal to 1mm.
Preferably, in the high-speed wire continuous rolling process, the billet after the coping process is rolled into a wire rod with the diameter of 5.5 to 17mm;
in the controlled cooling process, the wire rod is controlled and cooled by adopting a stelmor air cooling line, and the speed of a roller way is constant and is 0.2-1.0 m/s.
Preferably, the tensile strength of the wire rod after the cooling process is controlled to be 950-1200 MPa, the reduction of area is more than or equal to 50%, and the elongation after fracture is more than or equal to 15%.
Preferably, the metallographic structure of the wire rod after the controlled cooling step is a two-phase structure of pearlite and ferrite, wherein the volume fraction of pearlite is not less than 95%.
Preferably, the maximum depth of the decarburized layer of the wire rod after the controlled cooling step is less than or equal to 20 μm, and the number of surface defects in eddy current flaw detection is less than or equal to 10/ton.
Preferably, in the heat treatment process, the quenching process comprises a temperature rising section, a heat preservation section and a temperature reduction section, wherein the temperature of the temperature rising section rises from room temperature to the quenching temperature within 10s, the heat preservation time of the heat preservation section is 1 to 10s, and the cooling speed of the temperature reduction section is more than 50 ℃/s; the tempering process comprises a heating section, a temperature-equalizing section and a cooling section, wherein the temperature of the heating section is increased to the tempering temperature from room temperature within 10s, the heat preservation time of the temperature-equalizing section is 1-10s, and the cooling speed of the cooling section is 5-10 ℃/s.
In order to achieve the purpose, the invention further provides a 2100MPa grade spring steel wire which is prepared by the production method of the 2100MPa grade spring steel wire, wherein the diameter of the spring steel wire is 3.5-15mm, the tensile strength is larger than or equal to 2100MPa, and the reduction of area is larger than or equal to 48%.
Compared with the prior art, the invention has the beneficial effects that: based on the chemical component design and the full-flow control of the production process, the preparation of the 2100MPa grade spring steel wire can be realized, the tensile strength of the finally prepared spring steel wire is more than or equal to 2100MPa, the reduction of area is more than or equal to 48 percent, the high requirements of a large-load electric automobile suspension system on the strength and toughness of the spring steel wire in service can be met, and the technical problem that the toughness of the spring is reduced when the tensile strength of the spring is improved in the prior art is solved.
Detailed Description
The technical solution of the present invention is further described below with reference to specific embodiments, but the scope of protection claimed is not limited to the description.
The embodiment provides a production method of a 2100MPa grade spring steel wire and the 2100MPa grade spring steel wire prepared by the production method.
Specifically, the spring steel wire comprises the following chemical components in percentage by mass: 0.53 to 0.57 percent of C, 1.61 to 1.81 percent of Si, 0.7 to 0.8 percent of Mn, 0.81 to 0.91 percent of Cr, 0.11 to 0.19 percent of V, 0.02 to 0.04 percent of Nb, 0.01 to 0.09 percent of Ni, 0.01 to 0.10 percent of Mo, less than or equal to 0.002 percent of O, less than or equal to 0.003 percent of N, less than or equal to 0.002 percent of Al, less than or equal to 0.001 percent of Ti, less than or equal to 0.005 percent of Sn, less than or equal to 0.01 percent of S, less than or equal to 0.01 percent of P, less than or equal to 0.0002 percent of H, and the balance of Fe and inevitable impurities, wherein { [ V ] + [ Nb ] }/{ [ C ] + [ N ] } =0.23 to 0.4.
Specifically, the design principle of each chemical component is explained as follows.
C: the C content is 0.53 to 0.57 percent in the chemical composition design.
Si: the steel is a solid solution strengthening element, and can be used for reducing the oxygen content in steel and reducing inclusions, and in addition, si element can also block the elasticity decline in a spring; however, the plasticity of steel is reduced due to the excessively high Si content, the decarburization tendency of a billet is aggravated, the graphitization of cementite is promoted, and the fatigue resistance is influenced; in the chemical composition design of the invention, the Si content is 1.61-1.81%.
Mn: the solid solution strengthening element can improve the strength of the wire rod and can be combined with a harmful element S to reduce the hot brittleness of the wire rod; however, when the content of Mn is too high, hardenability is enhanced, a supercooled structure is easily formed, and the ductility and toughness of the material can be reduced; in the chemical composition design, the content of Mn is 0.7 to 0.8 percent.
Cr: the carbide forming element can improve the strength of steel, mainly exists in a cementite sheet layer in steel, and forms alloy cementite through replacement; when the Cr content is high, the wear resistance can be improved, the surface performance of steel is improved, but the hardenability is improved, and the ductility and toughness of the material are reduced; in the chemical composition design, the Cr content is 0.81 to 0.91 percent.
V: the alloy is an important carbide and nitride forming element, plays a role in fine grain strengthening and precipitation strengthening in steel, can also reduce the overheating sensitivity of steel, increase the tempering stability and optimize the strength and the plasticity of quenched and tempered steel; however, the degree of the strengthening effect of V is related to the content of N, and in the chemical composition design of the invention, the content of V is 0.11 to 0.19 percent.
Nb: the steel is a solid solution strengthening element, so that the spacing between austenite grains and pearlite lamellae can be refined, the quenching structure is refined, the tempering stability is increased, and the toughness is improved; but too much Nb can not be dissolved in steel, thereby improving the difficulty of controlling the quality of continuous casting billets and increasing the cost; in the chemical composition design of the invention, the Nb content is 0.02 to 0.04 percent.
Ni: the strength, low-temperature toughness and hardenability of the material are improved, but the cost of the Ni element is high; in the chemical composition design, the Ni content is 0.01 to 0.09 percent.
Mo: the addition of trace Mo can improve the hardenability of steel and is beneficial to improving the tempering resistance, but excessive Mo can form a large amount of carbides, so that the hardenability is reduced, and the cost is increased; in the chemical composition design of the invention, the content of Mo is 0.01 to 0.1 percent.
O: the steel mainly exists in the form of inclusions, the fatigue performance of the spring is greatly influenced, and the content of the inclusions is controlled within 0.002 percent.
N: the steel forms nitrides with V and Nb to precipitate and plays a role in strengthening, but the plasticity of the steel is reduced due to the excessively high content of N, and the content of N is controlled within 0.003%.
Al: is a deoxidizing element, is easy to form alumina inclusions, influences the fatigue performance of the spring steel, and the content of the aluminum inclusions is controlled within 0.002 percent.
Ti: the titanium oxide is easy to form as a precipitation strengthening element, affects the continuous casting and fatigue resistance of the billet, and the content of the titanium oxide is controlled within 0.001 percent.
Sn: the strength is improved, the plasticity is reduced, but the grain boundary bonding force is reduced, the surface quality of steel is not facilitated, the reticular cracks are easy to form, and the content of the reticular cracks is controlled within 0.005%.
S: besides easily causing center segregation, long-strip MnS inclusions are formed to reduce fatigue performance, and the content of the inclusions is controlled within 0.01 percent.
P: has strong segregation tendency, has great influence on product performance and tissue uniformity, and the content of the segregation tendency is controlled within 0.01 percent.
H: easy to cause hydrogen embrittlement, and is unfavorable for the mechanical property and fatigue resistance of steel, and the content of the hydrogen embrittlement is controlled within 0.0002 percent.
Further, { [ V ] + [ Nb ] }/{ [ C ] + [ N ] } =0.23 to 0.4, wherein [ V ] represents a mass percentage of V, [ Nb ] represents a mass percentage of Nb, [ C ] represents a mass percentage of C, and [ N ] represents a mass percentage of N. V and Nb play a role in fine grain strengthening and precipitation strengthening in steel, and can inhibit austenite crystal grain growth and refine pearlite sheet interlayer spacing by generating carbide and nitride precipitation, delay the decomposition of quenched martensite and the transformation of retained austenite, and be beneficial to optimizing the strength and plasticity of quenched and tempered steel, but the strengthening effect of V and Nb is influenced by the contents of C and N in steel, and C and N are beneficial to the strength of steel and are unfavorable to the plasticity; in the chemical composition design of the invention, the { [ V ] + [ Nb ] }/{ [ C ] + [ N ] } is controlled to be 0.23 to 0.4, so that the element strengthening effect of V and Nb can be fully exerted, and the steel has excellent strength and plasticity.
The following will specifically describe each step in the production method of the 2100MPa grade spring steel wire.
(1) Molten iron pre-desulfurization process
And desulfurizing the molten iron until S in the molten iron is less than or equal to 0.002 percent.
Preferably, the blast furnace molten iron is desulfurized in a KR desulphurization device, and the chemical components of the desulfurizing agent adopted in the molten iron pre-desulfurization process comprise, by mass: caO 70 to 85%, caF 2 5~10%，CaC 2 10 to 15 percent, and the balance of inevitable impurity components.
Preferably, the slagging-off rate of the desulfurization is more than or equal to 97 percent, and the temperature of the desulfurized molten iron is more than or equal to 1330 ℃.
(2) Converter smelting process
Smelting a smelting raw material consisting of scrap steel and pre-desulfurized molten iron in a converter, wherein the molten iron accounts for more than or equal to 85% of the smelting raw material by weight.
Specifically, molten iron and scrap steel after pre-desulfurization are mixed to form molten steel for desiliconization, dephosphorization, oxygen blowing and decarburization, then slag stopping and tapping are carried out, and a recarburizer, ferrosilicon and manganese metal are added into a steel ladle in the tapping process to carry out deoxidation alloying treatment on the molten steel.
(3) LF refining Process
And (3) sending the molten steel smelted by the converter into an LF furnace for smelting, adding refining slag and alloy into a steel ladle for chemical composition adjustment and inclusion adjustment, and tapping after the molten steel composition, the slag composition and the molten steel temperature all reach the standard. Wherein the alkalinity of the refining slag is 1.3 to 1.6, the types and the content of inclusions can be effectively controlled, the purity of molten steel is improved, and the fatigue resistance of the spring steel is improved.
Preferably, during the period of waiting for smelting, the flow of argon blown from the bottom of the steel ladle is 40 to 80NL/min, so that the slag surface fluctuates; when refined slag and alloy are added, the flow of argon blown from the bottom of the steel ladle is 200 to 600NL/min; and heating after the alloy is added so as to increase the temperature of the molten steel with the temperature reduced after the alloy is added, wherein the flow rate of argon blown to the bottom of the steel ladle during heating is 200 to 400 NL/min.
Preferably, the refining slag comprises the following chemical components in percentage by mass: 35 to 50 percent of CaO and SiO 2 25~35%，MgO 8~15%；CaF 2 12~20%；Al 2 O 3 ≤5%；T.Fe+MnO≤2%。
Preferably, the molten steel is alloyed by a low-aluminum low-titanium alloy.
(4) Vacuum refining step
After the vacuum treatment of the refining furnace, carrying out soft stirring on the molten steel, wherein the soft stirring time is more than or equal to 30min, and the bottom argon blowing flow of the steel ladle during the soft stirring is 40-150NL/min, so as to control the slight fluctuation of the slag surface and avoid the exposure of the molten steel.
(5) Continuous casting process of bloom
And (2) adopting bloom continuous casting to cast the molten steel into a continuous casting blank, adopting electromagnetic tail end stirring and continuous casting under high pressure, wherein the total reduction is 13-19mm, being beneficial to floating up inclusions, and reducing central segregation, and simultaneously realizing the great improvement of the purity of the continuous casting blank through the integral combination of a bloom continuous casting process and an LF refining process.
Specifically, the molten steel is allowed to stand on a continuous casting platform for more than 15min, then casting is carried out, full-protection casting is carried out by adopting a ladle long nozzle, an integral nozzle, a magnesium tundish covering agent and medium-carbon protective slag, the height of the liquid level of a crystallizer is 80 to 90 percent of the height of equipment, the continuous casting drawing speed is 0.5 to 0.63m/min, and the nitrogen increment in the continuous casting process is controlled to be less than or equal to 0.0002 percent. Wherein the section size of the continuous casting billet is 300mm multiplied by 390mm.
(6) Cogging procedure
Heating the continuous casting blank in a heating furnace, carrying out 9-pass continuous rolling, and cogging to form a small square blank with the cross section of 150mm multiplied by 150mm, wherein the heating temperature is 1150-1200 ℃, and the furnace time is less than or equal to 240min.
(7) Grinding process
And grinding the surface of the billet obtained in the cogging procedure, wherein the surface roughness Ra of the ground billet is less than or equal to 0.1 mu m.
Preferably, a grinder is used for carrying out coarse grinding and fine grinding on the surface of the small square billet in sequence, and the grinding depth of a single side is more than or equal to 1mm.
By the grinding and the control of the surface roughness of the billet, the surface defects of the billet and the decarburized layer formed by high-temperature heating in the cogging process can be basically eliminated, and the control of the surface quality in the subsequent high-speed wire rolling process is facilitated.
(8) High speed wire rolling process
Heating the small square billet in a heating furnace, then sending the small square billet to a twistless rolling machine, and rolling the small square billet into a wire rod with the diameter of 5.5 to 17mm, wherein the rolling temperature is 950 to 1050 ℃, and the spinning temperature is 850 to 900 ℃.
(9) Controlled cooling process
The cooling speed before pearlite transformation is 2.1-3.0 ℃/s, the pearlite transformation starting temperature is 650-750 ℃, the cooling speed in the pearlite transformation stage is less than or equal to 1 ℃/s, and the interlayer spacing of pearlite sheets is controlled to be less than or equal to 170nm.
Preferably, the steel wire rod is controlled and cooled by adopting a stelmor air cooling line, and the speed of a roller way is constant and is 0.2-1.0 m/s. Through the constant roller way speed, the surface defects caused by roller way friction can be effectively reduced.
In conclusion, based on the chemical component design, the whole control of the production process flow is combined, so that the mechanical property uniformity and the purity of the wire rod can be realized, the surface quality of the wire rod is improved, the maximum depth of a decarburized layer of the wire rod after the cooling process is controlled is less than or equal to 20 micrometers, the number of surface defect points of eddy current flaw detection is less than or equal to 10/ton, the tensile strength is 950 to 1200MPa, the reduction of area is more than or equal to 50 percent, the elongation after breakage is more than or equal to 15 percent, and the wire breakage rate of the spring steel wire prepared by further drawing can be effectively reduced; and the metallographic structure of the wire rod after the controlled cooling process is a pearlite and ferrite two-phase structure, wherein the volume fraction of the pearlite is more than or equal to 95%, so that the spring steel wire formed by further drawing the wire rod forms fine grains in the subsequent heat treatment process, the spring steel wire has high strength and excellent plasticity, the comprehensive performance is greatly improved, and the 2100MPa spring steel wire can be prepared for being used in an automobile suspension system.
(10) Acid washing process
Pickling the wire rod for 15 to 25min at the temperature of 20 to 30 ℃ by adopting 20% hydrochloric acid aqueous solution, then washing the wire rod by using clear water, and putting the wire rod into phosphating solution for phosphating treatment, wherein the mass of a film layer per unit area of a phosphating film is 10g/m 2 And after phosphating, washing the wire rod with water, and after saponification treatment by using soapy water, naturally drying the wire rod.
(11) Drawing step
And (3) cold-drawing the pickled wire rod into a steel wire with the diameter of 3.5-15mm by adopting dies with different diameters, wherein the pass reduction rate in drawing is more than 10%.
(12) Heat treatment Process
And sequentially quenching and tempering the steel wire obtained in the drawing process on a production line configured with online induction heating, wherein the quenching temperature is Ar3+ 20-Ar 3+50 ℃, ar3 is the austenitizing temperature of the wire rod, in the embodiment, the quenching temperature is 925-965 ℃, and the tempering temperature is 395-415 ℃, so that the energy consumption and the carbon emission can be reduced.
Preferably, the quenching process comprises a temperature rising section, a heat preservation section and a temperature reduction section, wherein the temperature of the temperature rising section rises from room temperature to the quenching temperature within 10s, the heat preservation time of the heat preservation section is 1 to 10s, and the cooling speed of the temperature reduction section is more than 50 ℃/s; the tempering process comprises a heating section, a temperature-equalizing section and a cooling section, wherein the temperature of the heating section is increased to the tempering temperature from room temperature within 10s, the heat preservation time of the temperature-equalizing section is 1-10s, and the cooling speed of the cooling section is 5-10 ℃/s.
Based on the chemical component design and the full-flow control of the production process, the preparation of the 2100MPa grade spring steel wire can be realized, the tensile strength of the finally prepared spring steel wire is more than or equal to 2100MPa, the reduction of area is more than or equal to 48 percent, the high requirements of a large-load electric automobile suspension system on the strength and toughness of the serving spring steel wire can be met, and the technical problem that the toughness of the spring is reduced when the tensile strength of the spring is improved in the prior art is solved.
The following examples further illustrate embodiments of the present invention. Of course, these 9 embodiments are only some, but not all, of the many variations that may be included in this embodiment.
Specifically, 9 examples each provide a spring steel wire whose chemical composition is shown in table 1.
[ Table 1]
Figure 179531DEST_PATH_IMAGE001
The production method of the present invention is obtained according to a large number of experimental studies, and each step in the production method is further described below with reference to specific 9 examples.
(1) Molten iron pre-desulfurization process
The blast furnace molten iron is adopted to carry out desulphurization in a KR desulphurization device, and the adopted desulphurization agent comprises the following chemical components in percentage by mass: caO 70 to 85%, caF 2 5~10%，CaC 2 10 to 15 percent, and the balance of inevitable impurity components; the slagging-off rate of the desulfurization is more than or equal to 97 percent, the temperature of the molten iron after the desulfurization is more than or equal to 1330 ℃, and the S in the molten iron is less than or equal to 0.002 percent.
(2) Converter smelting process
Carrying out desilicication, dephosphorization, oxygen blowing and decarburization on a smelting raw material formed by mixing the pre-desulfurized molten iron and scrap steel in a converter, wherein the molten iron accounts for more than or equal to 85% of the smelting raw material by weight percent; and then slag stopping and tapping, wherein a recarburizer, ferrosilicon and manganese metal are added into a steel ladle in the tapping process to deoxidize and alloy the molten steel.
(3) LF refining Process
And (3) delivering the molten steel smelted by the converter into an LF furnace for smelting, and adding refining slag and alloy into a ladle for chemical component adjustment and inclusion regulation until the molten steel components, the slag components and the molten steel temperature reach the standard, and then tapping. During the smelting period, the flow of argon blown from the bottom of the steel ladle is 40 to 80NL/min; when refined slag and alloy are added, the flow of argon blown from the bottom of the steel ladle is 200 to 600NL/min; and heating after the alloy is added so as to increase the temperature of the molten steel with the temperature reduced after the alloy is added, wherein the flow rate of argon blown from the bottom of the steel ladle during heating is 200 to 400 NL/min.
Specifically, the molten steel is alloyed by adopting a low-aluminum low-titanium alloy, and the refining slag comprises the following chemical components in percentage by mass: 35 to 50 percent of CaO and SiO 2 25~35%，MgO 8~15%；CaF 2 12~20%；Al 2 O 3 Less than or equal to 5 percent; T.Fe + MnO less than or equal to 2%, and the basicity of the refining slag is shown in Table 2.
(4) Vacuum refining step
After the vacuum treatment of the refining furnace, carrying out soft stirring on the molten steel, wherein the soft stirring time is more than or equal to 30min, and the bottom argon blowing flow of the steel ladle during the soft stirring is 40-150NL/min.
(5) Continuous bloom casting process
The method comprises the steps of adopting bloom continuous casting to cast molten steel into a continuous casting blank with the cross section size of 300mm multiplied by 390mm, specifically, standing the molten steel on a continuous casting platform for more than 15min, then casting, wherein the continuous casting adopts a ladle nozzle, an integral nozzle, a magnesium tundish covering agent and medium carbon protective slag to carry out full-protection casting, the height of a liquid level of a crystallizer is 80 to 90 percent of the height of equipment, the total pressure drop is shown in table 2 under electromagnetic tail end stirring and continuous casting high pressure, the continuous casting pulling speed is 0.5 to 0.63m/min, and the nitrogen increment in the continuous casting process is controlled to be less than or equal to 0.0002 percent.
(6) Cogging procedure
Heating the continuous casting blank in a heating furnace, carrying out 9-pass continuous rolling, and cogging to form a small square blank with the cross section of 150mm multiplied by 150mm, wherein the heating temperature is 1150-1200 ℃, and the furnace time is less than or equal to 240min.
(7) Grinding process
The surfaces of the small square billets obtained in the cogging procedure were subjected to coarse grinding and fine grinding successively by using a grinder, and the single-side grinding depth of the surfaces of the small square billets and the surface roughness Ra of the ground small square billets were shown in table 2.
(8) High speed wire rolling process
The billet was heated in a heating furnace and then sent to a twistless mill to be rolled into wire rods, the rolling temperature and the laying temperature are shown in table 2, and the diameter of the wire rods is shown in table 3.
(9) Controlled cooling process
The wire rod was cooled under control by means of stelmor air cooling line, and the cooling rate before pearlite transformation, the pearlite transformation starting temperature, the cooling rate at pearlite transformation stage, and the roller table speed were as shown in table 2, respectively.
[ Table 2]
Figure 565513DEST_PATH_IMAGE002
The metallographic structure of the wire rod after the controlled cooling step was examined, and it was found that the metallographic structure of the wire rod of 9 examples was a two-phase structure of pearlite and ferrite, and the volume fraction of pearlite is shown in table 3.
Respectively taking 10 samples from the head part, the middle part and the tail part of the wire rod after the controlled cooling process, respectively, preparing 30 samples in total to prepare a metallographic sample, placing the metallographic sample under a scanning electron microscope after mechanical polishing and nitric acid alcohol corrosion, amplifying by 10000 times, measuring the pearlite interlamellar spacing of a single sample, calculating the average value of the pearlite interlamellar spacing of the 30 samples to be used as the pearlite interlamellar spacing of the wire rod of each embodiment, and the pearlite interlamellar spacing of the wire rod of 9 embodiments is shown in table 3.
The maximum depth of the decarburized layer and the number of surface defects of the wire rod of 9 examples were measured as shown in Table 3.
The mechanical properties of the wire rods of the 9 examples were further measured, and the tensile strength, the reduction of area, and the elongation after fracture of the wire rods of the 9 examples are shown in table 3.
(10) Acid washing process
Pickling the wire rod for 15 to 25min at the temperature of 20 to 30 ℃ by adopting 20% hydrochloric acid aqueous solution, then washing the wire rod by using clear water, and putting the wire rod into phosphating solution for phosphating treatment, wherein the mass of a film layer per unit area of a phosphating film is 10g/m 2 And after phosphating, washing the wire rod with water, and naturally drying the wire rod after saponification treatment by using soapy water.
(11) Drawing process
And (3) cold-drawing the pickled wire rod into a steel wire with the diameter of 3.5-15mm by adopting dies with different diameters, wherein the pass reduction rate in drawing is more than 10%.
(12) Heat treatment Process
The steel wire obtained in the drawing step was quenched and tempered successively on a production line equipped with on-line induction heating, and the quenching temperature and the tempering temperature of 9 examples are shown in table 3, respectively.
Wherein the quenching process comprises a temperature rising section, a heat preservation section and a temperature reduction section, the temperature of the temperature rising section rises from room temperature to the quenching temperature within 10s, the heat preservation time of the heat preservation section is 1-10s, and the cooling speed of the temperature reduction section is more than 50 ℃/s; the tempering process comprises a heating section, a temperature-equalizing section and a cooling section, wherein the temperature of the heating section is increased to the tempering temperature from room temperature within 10s, the heat preservation time of the temperature-equalizing section is 1-10s, and the cooling speed of the cooling section is 5-10 ℃/s.
Further, mechanical properties of the steel wires after the heat treatment process were measured, and the tensile strength and the reduction of area of the steel wires of 9 examples were measured as shown in table 3.
[ Table 3]
Figure 312627DEST_PATH_IMAGE003
As can be seen from Table 3, the maximum depth of the decarburized layer of the wire rod after the cooling process in examples 1 to 9 produced according to the present embodiment was 20 μm or less, the number of surface defects in eddy current testing was 10/ton or less, the tensile strength was 950 to 1200MPa, the reduction of area was 50% or more, and the elongation after fracture was 15% or more; the steel wires in the embodiments 1 to 9 produced according to the present embodiment have a tensile strength of not less than 2100MPa and a reduction of area of not less than 48%, that is, the steel wire produced according to the present embodiment has a tensile strength of 2100MPa, which realizes difficulty spanning from 2000MPa to 2100MPa, and has excellent toughness when used for spring steel wires, so as to satisfy high requirements of a high-load electric vehicle suspension system on the strength and toughness of the spring steel wire in service, and overcome the technical problem that the existing production technology can cause the toughness to be reduced while improving the tensile strength of the spring.
The above description is only for the preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art should be considered as the technical solutions and the inventive concepts of the present invention within the technical scope of the present invention.

Claims (9)

1. A production method of a 2100MPa grade spring steel wire is characterized in that the spring steel wire comprises the following chemical components in percentage by mass: 0.53 to 0.57 percent of C, 1.61 to 1.81 percent of Si, 0.7 to 0.8 percent of Mn, 0.81 to 0.91 percent of Cr, 0.11 to 0.19 percent of V, 0.02 to 0.04 percent of Nb, 0.01 to 0.09 percent of Ni, 0.01 to 0.10 percent of Mo, less than or equal to 0.002 percent of O, less than or equal to 0.003 percent of N, less than or equal to 0.002 percent of Al, less than or equal to 0.001 percent of Ti, less than or equal to 0.005 percent of Sn, less than or equal to 0.01 percent of S, less than or equal to 0.01 percent of P, less than or equal to 0.0002 percent of H, and the balance of Fe and inevitable impurities, wherein { [ V ] + [ Nb ] }/{ [ C ] + [ N ] } =0.23 to 0.4; the production method comprises the working procedures of molten iron pre-desulfurization, converter smelting, LF refining, vacuum refining, bloom continuous casting, cogging, coping, high-speed wire rolling, controlled cooling, acid washing, drawing and heat treatment which are sequentially carried out; wherein:
in the LF refining process, the alkalinity of refining slag is 1.3 to 1.6;
in the continuous casting process of the large square billet, stirring by adopting an electromagnetic tail end and carrying out continuous casting under a large pressure, wherein the total pressure reduction is 13 to 19mm;
in the coping process, the surface of the small square billet obtained in the blank opening process is grinded, and the surface roughness Ra of the grinded small square billet is less than or equal to 0.1 mu m;
in the high-speed wire rolling process, the billet is rolled into a wire rod, the rolling temperature is 950 to 1050 ℃, and the spinning temperature is 850 to 900 ℃;
in the controlled cooling process, the cooling speed before pearlite transformation is 2.1-3.0 ℃/s, the pearlite transformation starting temperature is 650-750 ℃, the cooling speed in the pearlite transformation stage is less than or equal to 1 ℃/s, the metallographic structure of the wire rod after the controlled cooling process is a two-phase structure of pearlite and ferrite, wherein the volume fraction of the pearlite is more than or equal to 95%, and the interlayer spacing of pearlite sheets is controlled to be less than or equal to 170nm;
in the heat treatment process, the steel wire obtained in the drawing process is quenched and tempered in sequence on a production line configured with on-line induction heating, wherein the quenching temperature is Ar < 3+ > 20-Ar < 3+ >50 ℃, ar < 3 > is the austenitizing temperature of the steel wire, and the tempering temperature is 395-415 ℃.
2. The production method of the 2100MPa grade spring steel wire according to claim 1, characterized in that in the molten iron pre-desulfurization process, molten iron is desulfurized until S in the molten iron is less than or equal to 0.002%;
in the converter smelting process, smelting raw materials consisting of scrap steel and pre-desulfurized molten iron in a converter, wherein the molten iron accounts for more than or equal to 85% of the smelting raw materials by weight;
in the LF refining process, low-aluminum low-titanium alloy is adopted to carry out alloying treatment on molten steel;
in the vacuum refining process, after the vacuum treatment is carried out in the refining furnace, the molten steel is subjected to soft stirring, and the soft stirring time is more than or equal to 30min.
3. The production method of the 2100MPa grade spring steel wire according to claim 1, characterized in that in the cogging procedure, the continuous casting billet is heated in a heating furnace and then is subjected to 9 times of continuous rolling, and is cogging into a small square billet with the cross section of 150mm x 150mm, the heating temperature is 1150-1200 ℃, and the furnace time is less than or equal to 240min.
4. The 2100MPa grade spring steel wire production method according to claim 1, characterized in that in the grinding process, a grinder is adopted to perform coarse grinding and fine grinding on the surface of the small square billet in sequence, and the single-side grinding depth is more than or equal to 1mm.
5. The 2100MPa grade spring steel wire production method according to claim 1, characterized in that in the high wire continuous rolling process, the billet after the coping process is rolled into a wire rod with the diameter of 5.5 to 17mm;
in the controlled cooling process, the steel wire rod is controlled and cooled by adopting a stelmor air cooling line, and the speed of a roller way is constant and is 0.2-1.0 m/s.
6. The production method of the 2100MPa grade spring steel wire according to claim 5, wherein the tensile strength of the wire rod after the controlled cooling process is 950-1200 MPa, the reduction of area is more than or equal to 50%, and the elongation after fracture is more than or equal to 15%.
7. The method for producing a 2100MPa grade spring steel wire according to claim 5, wherein the maximum depth of the decarburized layer of the wire rod after the controlled cooling process is not more than 20 μm, and the number of surface defects in eddy current testing is not more than 10/ton.
8. The production method of the 2100MPa grade spring steel wire according to claim 1, characterized in that in the heat treatment process, the quenching process comprises a temperature rising section, a temperature holding section and a temperature reduction section, the temperature of the temperature rising section rises from room temperature to the quenching temperature within 10s, the temperature holding time of the temperature holding section is 1-10s, and the cooling speed of the temperature reduction section is more than 50 ℃/s; the tempering process comprises a heating section, a temperature-equalizing section and a cooling section, wherein the temperature of the heating section is increased to the tempering temperature from room temperature within 10s, the heat preservation time of the temperature-equalizing section is 1-10s, and the cooling speed of the cooling section is 5-10 ℃/s.
9. A2100 MPa grade spring steel wire is characterized by being prepared by the production method of the 2100MPa grade spring steel wire according to any one of claims 1 to 8, the diameter of the spring steel wire is 3.5 to 15mm, the tensile strength is larger than or equal to 2100MPa, and the reduction of area is larger than or equal to 48%.
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