CN111321342A - One-steel multi-stage cold-rolled low-alloy high-strength steel and manufacturing method thereof - Google Patents
One-steel multi-stage cold-rolled low-alloy high-strength steel and manufacturing method thereof Download PDFInfo
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- CN111321342A CN111321342A CN202010132475.1A CN202010132475A CN111321342A CN 111321342 A CN111321342 A CN 111321342A CN 202010132475 A CN202010132475 A CN 202010132475A CN 111321342 A CN111321342 A CN 111321342A
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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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- 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
- C21D1/26—Methods of annealing
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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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/003—Cementite
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/009—Pearlite
Abstract
The invention relates to a multi-stage cold-rolled low-alloy high-strength steel, which comprises the following chemical components in percentage by mass: c: 0.04-0.07%, Si: 0.1-0.3%, Mn: 0.4-0.6%, P is less than or equal to 0.018%, S is less than or equal to 0.010%, Als: 0.020-0.060%, Ti: 0.010-0.020%, and the balance of Fe and inevitable impurities. The invention also relates to a production method of the multi-stage cold-rolled low-alloy high-strength steel, which comprises the working procedures of continuous casting, hot rolling, acid rolling, continuous annealing and leveling, wherein in the hot rolling process, the plate blank is heated to 1220-; and respectively adopting different parameter ranges for laminar cooling, continuous annealing temperature and flat elongation after rolling according to different grades of the produced low-alloy high-strength steel. The invention can realize the production of the multi-level low-alloy high-strength steel plate with the yield strength of 210-260MPa by using the steelmaking components, and reduce the production cost of enterprises.
Description
Technical Field
The invention relates to the technical field of high-strength steel production, in particular to multi-stage cold-rolled low-alloy high-strength steel and a manufacturing method thereof.
Background
Low alloy steels are steels which are formed by adding alloying elements with a content of generally less than 3wt% based on ordinary carbon steel, and are called low alloy high strength steels because the strength of such steels is significantly higher than that of carbon steels with the same carbon content.
At present, cold-rolled low-alloy high-strength steel is produced by adopting a Nb and Ti composite component system through a continuous annealing process, and the refining effect of Nb on crystal grains and the dispersion precipitation effect of Ti are utilized to achieve a certain strength level; for example, the Chinese patent application No. 201811246544.0 entitled "280 MPa-grade cold-rolled low-alloy high-strength steel and manufacturing method thereof" adds 0.030-0.060 wt% of Nb element; the Chinese patent application No. 201510241619.6, entitled 260-grade 330-grade low-alloy high-strength steel production method, adds Ti with the weight percent less than or equal to 0.020% and Nb with the weight percent less than or equal to 0.020% to achieve the required strength. The simultaneous addition of a plurality of alloy elements is not beneficial to the reduction of the production cost of the automobile sheet.
In addition, the low-alloy high-strength steel is widely applied to parts such as structural parts and reinforcing parts of stamping automobiles, although automobile factories have more requirements on cold-rolled low-alloy high-strength steel with different grades and specifications, the ordering quantity of the steel with the same grade is less, the ordering quantity is about 80 tons each time, the steel of 1 furnace of steel enterprise organization production is about 100 plus 250 tons according to the furnace volume, residual slab waste is caused, meanwhile, the low-alloy high-strength steel with different strength grades adopts different alloy components, the utilization rate of the slab is not favorably improved, a large amount of mixed casting slabs are caused, the continuous production of the steel enterprise is not favorably realized, and the production cost is increased.
Disclosure of Invention
The invention aims to solve the technical problem of providing the multi-stage cold-rolled low-alloy high-strength steel and the manufacturing method thereof, and the multi-stage low-alloy high-strength steel plate with the yield strength covering 210-260MPa level is produced by steelmaking components through measures of replacing Nb with Ti and improving the production process, so that the production cost of enterprises is reduced.
The technical scheme for solving the technical problems is as follows:
the multistage cold-rolled low-alloy high-strength steel comprises the following chemical components in percentage by mass: c: 0.03-0.08%, Si: 0.1-0.3%, Mn: 0.4-0.6%, P is less than or equal to 0.018%, S is less than or equal to 0.010%, Als: 0.020-0.060%, Ti: 0.010-0.030%, and the balance of Fe and inevitable impurities.
In the above one-steel multi-stage cold-rolled low-alloy high-strength steel, the mass percentage of C, Ti elements in the chemical composition is preferably C: 0.04-0.07%, Ti: 0.010-0.020% to reduce cost and improve product stability.
The one-steel multi-stage cold-rolled low-alloy high-strength steel comprises a 210MPa level, a 240MPa level and a 260MPa level; the thickness is 0.6-2.5mm, and the microstructure is ferrite, pearlite and cementite; when the 210 MPa-grade low-alloy high-strength steel is produced, the yield strength range is 210-410 MPa, the tensile strength is 310-410MPa, and the elongation after fracture is more than or equal to 30 percent; when the 240 MPa-level low-alloy high-strength steel is produced, the yield strength is 240-plus-300 MPa, the tensile strength is 320-plus-420 MPa, and the elongation after fracture is more than or equal to 28 percent; when the 260 MPa-grade low-alloy high-strength steel is produced, the yield strength is 260-320MPa, the tensile strength is 350-430MPa, and the elongation after fracture is more than or equal to 26 percent.
The manufacturing method of the steel multi-stage cold-rolled low-alloy high-strength steel comprises the working procedures of continuous casting, hot rolling, acid rolling, continuous annealing and leveling, wherein the continuous casting billet comprises the following chemical components in percentage by mass: c: 0.04-0.07%, Si: 0.1-0.3%, Mn: 0.4-0.6%, P is less than or equal to 0.018%, S is less than or equal to 0.010%, Als: 0.020-0.060%, Ti: 0.010-0.020%, and the balance of Fe and inevitable impurities.
The manufacturing method of the one-steel multi-stage cold-rolled low-alloy high-strength steel comprises the following hot rolling process: heating the slab to 1220-.
The manufacturing method of the one-steel multi-stage cold-rolled low-alloy high-strength steel comprises the following hot rolling process: respectively cooling the rolled steel by a laminar cooling system, and cooling the rolled steel to the temperature of 620-650 ℃ for coiling when 210 MPa-level low-alloy high-strength steel is produced; when 240 MPa-grade low-alloy high-strength steel is produced, cooling to 590-620 ℃ for coiling; when producing 260MPa grade low alloy high strength steel, cooling to 560-.
The manufacturing method of the one-steel multi-stage cold-rolled low-alloy high-strength steel comprises the following steps: the reduction rate of acid rolling is controlled to be 55-80%; when the steel plate is produced at the level of 210MPa, the annealing temperature of the steel plate is 820-840 ℃; when the steel plate is produced at the 240MPa level, the annealing temperature of the steel plate is 800-820 ℃; when the steel plate is produced at 260MPa, the annealing temperature of the steel plate is 780-800 ℃; the annealing time is 80-140 s, and the annealing speed is 140-200 m/min; cooling in a slow cooling and rapid cooling mode after annealing, wherein the cooling speed is 3-6 ℃/s to firstly cool to 660-420 ℃, and then the cooling speed is 45-55 ℃/s to rapidly cool to 380-420 ℃; carrying out overaging treatment at the temperature of 370-330 ℃; final cooling is carried out, and the final cooling temperature is less than or equal to 150 ℃.
According to the manufacturing method of the multi-stage cold-rolled low-alloy high-strength steel, the flattening is performed after the final cooling process, and the flattening elongation rates are respectively as follows: the steel plate with the 210MPa grade is 1.1-1.4%; the steel plate of 240MPa grade is 1.2-1.5%; the steel plate with the grade of 260MPa is 1.3-1.6%.
According to the invention, through component optimization, a single Ti alloy element is adopted, and the dispersion precipitation strengthening effect of the Ti element with lower cost is utilized to replace the refined grain strengthening effect of the Nb element with higher cost, so that the alloy cost is degraded, the one-steel multi-stage cold-rolled low-alloy high-strength steel with the yield strength covering the level of 210-260MPa is obtained, the thickness is 0.6-2.5mm, and the microstructure is ferrite, pearlite and cementite; when the yield strength is 210MPa, the yield strength range is 210-270MPa, the tensile strength is 310-410MPa, and the elongation after fracture is more than or equal to 30 percent; when the yield strength is 240MPa, the yield strength range is 240-300MPa, the tensile strength is 320-420MPa, and the elongation after fracture is more than or equal to 28 percent; when the yield strength is 260MPa, the yield strength range is 260-.
The invention adds single Ti microalloying element, and carbon and nitrogen compounds formed by the Ti microalloying element and the carbon and the nitrogen are separated out at a phase interface during the transformation from austenite to ferrite, thereby effectively preventing the growth of ferrite grains and playing a role in refining the grains; when the Ti content reaches a certain value, precipitation hardening effect can be generated due to dispersion and precipitation of the ferrotitanium compound. The invention replaces the grain refining strengthening effect of Nb element with higher cost with the dispersion precipitation strengthening effect of Ti element with lower cost, some titanium is needed to be considered to be consumed in forming insoluble titanium nitride TiN and not participate in precipitation strengthening, the strength can not be improved by adding Ti with less than 0.01wt%, and the Ti content is finally selected to be 0.010-0.020 wt%.
The coiling temperature is controlled, the coiling temperature with the yield strength of 210MPa grade is 620-650 ℃, the coiling temperature with the yield strength of 240MPa grade is 590-620 ℃, and the coiling temperature with the yield strength of 260MPa grade is 560-590 ℃, because most of the nucleation and growth of proeutectoid ferrite are completed under the condition of extremely slow cooling from the coiling temperature, and the isothermal transformation process is approximately considered, therefore, when the coiling temperature is higher, ferrite grains are coarse and uniform, the strength of the strip steel with the lower coiling temperature is improved, and the head-tail uniformity is better.
The continuous annealing temperature is controlled, the annealing temperature of the yield strength of 210MPa level is 820-.
The invention adopts a cooling mode of slow cooling and quick cooling to slowly cool to 660-680 ℃, so that the internal stress of the product is reduced during the cooling process, the buckling deformation of the product caused by the sudden temperature reduction of the strip steel in the cooling process from the high-temperature recrystallization temperature is prevented, and the product keeps good plate shape; then rapidly cooling to 380-420 ℃, and the operation aims to rapidly cool to the target temperature, control the solid solution carbon content of the final product and finally control the performance of the finished product.
The invention adopts the aging treatment, because the aging treatment has the functions of enabling the carbide in the steel to be evenly precipitated and distributed in the crystal, reducing the content of solid solution carbon in the steel and reducing the aging property of the finished steel plate, and the temperature of the aging treatment is between 370 ℃ and 330 ℃.
The leveling process is adopted, and the yield platform can be eliminated after a certain deformation degree is ensured by setting the proper leveling elongation, so that the orange peel phenomenon can not occur in the use process of the strip steel, and the yield strength is improved. Materials of different strength grades have slightly different flattening processes according to the strength range.
The invention has the beneficial effects that:
on the basis of low C, the invention utilizes Ti with lower cost to replace Nb with higher cost, and the component design ideas of Ti micro-alloying and Mn and Si solid solution strengthening effectively reduce the alloy cost.
The invention achieves the purpose of simultaneously obtaining cold-rolled low-alloy high-strength steel products with yield strengths of 210MPa, 240MPa and 260MPa by adopting one steel-making component through proper hot rolling and cold rolling process parameters.
The manufacturing method of the invention can enable iron and steel enterprises to realize one-steel production of multi-level products, thereby not only reducing the waste of smelting residual plate blanks, but also reducing the generation of mixed casting blanks in the smelting process of low alloy steel high-strength steel with different strengths, and creating benefits for the enterprises.
Drawings
FIG. 1 is a metallographic structure diagram (1000 ×) of a steel sheet produced in example 1 and having a yield strength of 210MPa class;
FIG. 2 is a metallographic structure chart (1000 ×) showing the yield strength of 240MPa class of the steel sheet produced in example 6.
FIG. 3 is a metallographic structure chart (1000 ×) showing the structure of a steel sheet having a yield strength of 260MPa grade produced in example 11.
Detailed Description
The invention is further illustrated by the following specific examples:
specific examples 1 to 10 chemical compositions of continuous cast slabs for low alloy high strength steel are shown in table 1:
TABLE 1 chemical composition (wt%)
The control range of the hot rolling process parameters comprises the hot rolling heating temperature of 1220-:
TABLE 2 Hot Rolling Process parameters
In the cold rolling continuous annealing process and the flattening process, the control range of the soaking temperature in continuous annealing is 820-:
TABLE 3 continuous annealing Process parameters
Table 4 lists the mechanical properties of the low alloy, high strength steel products of examples 1-10:
TABLE 4 mechanical Properties of the products
Through performance inspection, the yield strength of the embodiment 1-5 is within the range of 210-410 MPa, the tensile strength is within the range of 310-410MPa, and the elongation after fracture meets the requirement of more than or equal to 30 percent; the yield strength of the examples 6 to 10 is in the range of 240-300MPa, the tensile strength is in the range of 320-420MPa, the elongation after fracture meets the requirement of being more than or equal to 28 percent, the yield strength of the examples 11 to 15 is in the range of 260-320MPa, the tensile strength is in the range of 350-430MPa, and the elongation after fracture meets the requirement of being more than or equal to 26 percent, so that the requirement of the yield strength covering the one-steel multi-stage cold-rolled low-alloy high-strength steel of the level of 210-260MPa is met.
Fig. 1-3 show that the microstructure of the low-alloy high-strength steel produced by the invention is ferrite, pearlite and cementite.
Claims (8)
1. The multi-stage cold-rolled low-alloy high-strength steel is characterized by comprising the following components in percentage by weight: the low-alloy high-strength steel comprises the following chemical components in percentage by mass: c: 0.03-0.08%, Si: 0.1-0.3%, Mn: 0.4-0.6%, P is less than or equal to 0.018%, S is less than or equal to 0.010%, Als: 0.020-0.060%, Ti: 0.010-0.030%, and the balance of Fe and inevitable impurities.
2. The one-steel multi-stage cold-rolled low-alloy high-strength steel as claimed in claim 1, wherein: the chemical components comprise the following components in percentage by mass: c: 0.04-0.07%, Si: 0.1-0.3%, Mn: 0.4-0.6%, P is less than or equal to 0.018%, S is less than or equal to 0.010%, Als: 0.020-0.060%, Ti: 0.010-0.020%, and the balance of Fe and inevitable impurities.
3. The manufacturing method of the steel multi-stage cold-rolled low-alloy high-strength steel comprises the working procedures of continuous casting, hot rolling, acid rolling, continuous annealing and leveling, and is characterized in that: the continuous casting billet comprises the following chemical components in percentage by mass: c: 0.04-0.07%, Si: 0.1-0.3%, Mn: 0.4-0.6%, P is less than or equal to 0.018%, S is less than or equal to 0.010%, Als: 0.020-0.060%, Ti: 0.010-0.020%, and the balance of Fe and inevitable impurities.
4. The method for manufacturing the one-steel multi-stage cold-rolled low-alloy high-strength steel as claimed in claim 3, wherein: the hot rolling step: heating the slab to 1220-.
5. The manufacturing method of the one-steel multi-stage cold-rolled low-alloy high-strength steel as claimed in claim 4, wherein the hot rolling process comprises the following steps: respectively cooling the rolled steel by a laminar cooling system, and cooling the rolled steel to the temperature of 620-650 ℃ for coiling when 210 MPa-level low-alloy high-strength steel is produced; when 240 MPa-grade low-alloy high-strength steel is produced, cooling to 590-620 ℃ for coiling; when producing 260MPa grade low alloy high strength steel, cooling to 560-.
6. The method for manufacturing the one-steel multi-stage cold-rolled low-alloy high-strength steel as claimed in claim 3, wherein: the acid rolling process comprises the following steps: the reduction rate of acid rolling is controlled to be 55-80%; when the steel plate is produced at the level of 210MPa, the annealing temperature of the steel plate is 820-840 ℃; when the steel plate is produced at the 240MPa level, the annealing temperature of the steel plate is 800-820 ℃; when the steel plate is produced at 260MPa, the annealing temperature of the steel plate is 780-800 ℃; the annealing time is 80-140 s, and the annealing speed is 140-200 m/min; cooling in a slow cooling and rapid cooling mode after annealing, wherein the cooling speed is 3-6 ℃/s to firstly cool to 660-420 ℃, and then the cooling speed is 45-55 ℃/s to rapidly cool to 380-420 ℃; carrying out overaging treatment at the temperature of 370-330 ℃; final cooling is carried out, and the final cooling temperature is less than or equal to 150 ℃.
7. The method for manufacturing the one-steel multi-stage cold-rolled low-alloy high-strength steel as claimed in claim 3, wherein: and (3) leveling after the final cooling process, wherein the leveling elongation rates are respectively as follows: the steel plate with the 210MPa grade is 1.1-1.4%; the steel plate of 240MPa grade is 1.2-1.5%; the steel plate with the grade of 260MPa is 1.3-1.6%.
8. The one-steel multi-stage cold-rolled low-alloy high-strength steel as claimed in claim 1 or 3, wherein: the low-alloy high-strength steel comprises 210MPa grade, 240MPa grade and 260MPa grade; the thickness is 0.6-2.5mm, and the microstructure is ferrite, pearlite and cementite; when the 210 MPa-grade low-alloy high-strength steel is produced, the yield strength range is 210-410 MPa, the tensile strength is 310-410MPa, and the elongation after fracture is more than or equal to 30 percent; when the 240 MPa-level low-alloy high-strength steel is produced, the yield strength is 240-plus-300 MPa, the tensile strength is 320-plus-420 MPa, and the elongation after fracture is more than or equal to 28 percent; when the 260 MPa-grade low-alloy high-strength steel is produced, the yield strength is 260-320MPa, the tensile strength is 350-430MPa, and the elongation after fracture is more than or equal to 26 percent.
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| CN114196878A (en) * | 2021-11-19 | 2022-03-18 | 广西钢铁集团有限公司 | Production method for producing low-cost flexible low-carbon aluminum killed steel with three different yield strength grades on same production line |
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Application publication date: 20200623 |