CN113416893B - High-strength high-plasticity ferrite-austenite dual-phase cold-rolled steel plate for automobile and production method thereof - Google Patents
High-strength high-plasticity ferrite-austenite dual-phase cold-rolled steel plate for automobile and production 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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- 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
- 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
- C21D8/02—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
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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
- C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
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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
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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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
- C21D2211/001—Austenite
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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
Abstract
The invention relates to a high-strength high-plasticity ferrite-austenite dual-phase cold-rolled steel plate for automobiles and a production method thereof, wherein the cold-rolled steel plate comprises the following chemical components in percentage by mass: c:0.2% -0.4%, cu:1.0% -2.0%, mn: 6-8%, al: 0.4-0.8%, P <0.020%, S <0.006%, and the balance Fe and inevitable impurities. The advantages are that: by utilizing the alloying of Al and Cu, inhibiting the precipitation of cementite and expanding the austenite phase region of Cu, and controlling rolling and annealing treatment, a proper amount of austenite content is obtained, and excellent performances of 980-1180MPa of tensile strength and more than 30-35% of elongation are obtained.
Description
Technical Field
The invention belongs to the field of cold-rolled steel plates, and particularly relates to a high-strength high-plasticity ferrite-austenite dual-phase cold-rolled steel plate for an automobile and a production method thereof, wherein the ferrite-austenite dual-phase cold-rolled steel plate is applied to manufacturing of automobile structural parts.
Background
The automobile industry is further developed towards light weight and low pollution, and the automobile steel has the preferential development direction of high strength and high plasticity. Phase diagram calculation, multi-alloying, controlled rolling and heat treatment have become the most important technical means for manufacturing high-strength and high-plasticity automobile steel.
In the prior art, a Chinese patent with publication number CN 106834942A 'copper-containing nano-phase reinforced medium manganese steel and a preparation method thereof' contains Cu, al and Si, and also adds Ni, W, mo and Ti elements, so that the alloy cost is high. The C content is below 0.1%, and the casting and rolling difficulty is increased.
The Chinese patent with publication number CN109930078A 'a high-strength high-plasticity hot-rolled medium manganese steel' has 5% of manganese content, 4% of aluminum content and too high aluminum content, water gap blockage is easy to occur during continuous casting, and the risk of hot rolling cracking of a steel plate is increased.
The chinese patent with the application number of cn201310681656.X, "a high-strength high-plasticity cold-rolled medium manganese steel and a preparation method thereof," still contains high aluminum in addition to high Mn content, and is not favorable for industrial production.
The publication number is CN103695765A 'a high-strength high-plasticity cold-rolled medium manganese steel and a preparation method thereof', the component design has high manganese content, single microalloying is adopted, the production difficulty is high, and the microalloying effect is limited.
Disclosure of Invention
In order to overcome the defects of the prior art, the invention aims to provide a high-strength high-plasticity ferrite-austenite dual-phase cold-rolled steel plate for an automobile and a production method thereof.
In order to achieve the purpose, the invention is realized by the following technical scheme:
a high-strength high-plasticity ferritic-austenitic dual-phase cold-rolled steel sheet for automobiles comprises the following chemical components in percentage by mass:
c: 0.2-0.4%, si less than or equal to 0.1%, cu:1.0% -2.0%, mn: 6-8%, al:0.4 to 0.8 percent of Fe, less than 0.020 percent of P, less than 0.006 percent of S and the balance of Fe and inevitable impurities.
A production method of a high-strength high-plasticity ferrite-austenite dual-phase cold-rolled steel plate for automobiles comprises the following steps:
1) And (3) heating process: heating the billet steel to 1000 +/-50 ℃ in a heating furnace, and preserving heat for 2 +/-0.5 hours;
2) The rolling process comprises the following steps: adopting common rolling and laminar cooling, wherein the final rolling temperature is 680 +/-30 ℃, and ensuring the coiling temperature to be 610 +/-30 ℃;
3) The cold rolling process comprises the following steps: the total cold rolling reduction is not lower than 60%;
4) Annealing process: the annealing temperature is 800 +/-10 ℃, the temperature is kept for 3 +/-0.5 minutes, the mixture is cooled to the room temperature at the cooling speed of 25 +/-5 ℃/s, the temperature is kept constant at 620-650 ℃ for 10 +/-1.0 minutes, and the mixture is cooled to the room temperature along with the furnace.
Based on cost and manufacturing difficulty, the steel plate provided by the invention comprises the following components in parts by weight:
c: carbon is the most important solid solution strengthening and stabilizing austenite element in steel, and a certain amount of solid solution carbon can ensure the strength and the proper microstructure. The carbon content is too high, which is disadvantageous in formability and weldability of the steel sheet. If the carbon content is too low, it is difficult to ensure the strength of the steel and to control the microstructure properly. The optimal range of carbon is 0.2% -0.4%.
Mn: manganese is used for solid solution strengthening, austenite phase region expansion and austenite stabilization. However, too high a manganese content results in a single austenite structure, increasing cost and increasing manufacturing difficulty, and too low a manganese content does not result in a suitable microstructure. The content of manganese in the invention is 6-8%.
Al: aluminum can form a matrix which inhibits cementite precipitation, fixes nitrogen in steel and plays a certain role in refining grains, but excessive aluminum increases the continuous casting difficulty, so the range of aluminum content is Al:0.4 to 0.8 percent.
Cu: the method has the advantages that the austenite phase region is enlarged, the weather resistance and the weldability of the steel are improved, the strength of the steel is improved by precipitation in a body, but the hot brittleness is caused by overhigh content, the beneficial effect cannot be exerted by overlow content, and the optimal range of the copper content is 1.0-2.0%.
P: although phosphorus can improve the strength of the steel sheet, it seriously deteriorates cold formability of the steel, particularly secondary formability, and is limited to 0.020%.
Si: the low Si design is selected because the generation of cementite is suppressed and the strength is improved, but the surface quality of the steel is deteriorated.
S: sulfur is a harmful element in steel and forms manganese sulfide to deteriorate the properties of steel sheet, so that the content thereof is preferably as small as possible, and is limited to 0.006%.
Compared with the prior art, the invention has the beneficial effects that:
on the basis of the component design of the medium manganese steel, the invention utilizes the alloying of Al and Cu to inhibit the precipitation of cementite and the expansion of Cu in an austenite phase region, and obtains a proper amount of austenite content by controlling rolling and annealing treatment, thereby obtaining the dual-phase automobile steel with the tensile strength of 980-1180MPa, the elongation of more than 30-35 percent, and good formability, weather resistance and weldability.
Drawings
FIG. 1 is a gold phase diagram of the present invention.
Detailed Description
The present invention will be described in detail below with reference to the accompanying drawings, but it should be noted that the present invention is not limited to the following embodiments.
Referring to fig. 1, the high-strength and high-plasticity ferritic-austenitic dual-phase cold-rolled steel sheet for the automobile comprises the following chemical components in percentage by mass:
c:0.2% -0.4%, cu:1.0% -2.0%, mn:6% -8%, al: 0.4-0.8%, P <0.020%, S <0.006%, and the balance Fe and inevitable impurities.
The production method of the high-strength high-plasticity ferritic-austenitic dual-phase cold-rolled steel plate for the automobile comprises the following steps of:
1) A heating process: heating the steel billet in a heating furnace to 1000 +/-50 ℃, and preserving heat for 2 +/-0.5 hours to ensure that alloy elements are fully dissolved in a solid manner, the components are uniform, the oxidation burning loss of the steel billet is reduced, and the surface defect of the steel plate caused by copper elements with low melting point is avoided;
2) The rolling process comprises the following steps: common rolling and continuous laminar cooling are adopted, the finish rolling temperature is 680 +/-30 ℃, the coiling temperature is guaranteed to be 610 +/-30 ℃, deformation induced ferrite can be generated, mn is diffused from the ferrite to austenite through short-circuit diffusion, the austenite is further stabilized, and a certain amount of austenite is contained in the microstructure of the hot-rolled steel plate;
3) The cold rolling process comprises the following steps: the total cold rolling reduction is not lower than 60%;
4) Annealing process: keeping the temperature at 800 + -10 ℃ for 3 + -0.5 minutes, cooling to room temperature at 25 + -5 ℃/s, keeping the temperature at 620-650 ℃ for 10 + -1.0 minutes, and cooling to room temperature along with the furnace.
The specific production method comprises the following steps: cutting the head and the tail of a casting blank with qualified components of 80kg, heating to 1000 +/-50 ℃, and preserving heat for 4 hours. The hot rolling finishing temperature is 680 +/-30 ℃, the simulated coiling temperature is 610 +/-30 ℃, the temperature is kept for 8 hours, and the thickness of the hot rolled plate is 4.5mm. Hot rolling, acid washing, cold rolling to 1.0-1.5mm, keeping the temperature at 800 + -10 deg.C for 3 + -0.5 min, cooling to room temperature at a temperature not lower than 25 deg.C/s, heating to 620-650 deg.C, keeping the temperature for 10 + -1.0 min, and furnace cooling to room temperature.
The specific components, process system and properties of the steel sheets of the 6 examples are shown in tables 1 to 3.
TABLE 1 chemical composition of inventive examples (wt%)
TABLE 2 Hot Rolling Process, cold Rolling reduction and annealing Process according to the examples of the present invention
TABLE 3 mechanical Property parameters of the examples of the invention
On the basis of the component design of the medium manganese steel, the invention utilizes the alloying of Al and Cu to inhibit the precipitation of cementite and the expansion of Cu in an austenite phase region, and obtains a proper amount of austenite content by controlling rolling and annealing treatment, thereby obtaining the dual-phase automobile steel with the tensile strength of 980-1180MPa, the elongation of more than 30-35 percent, and good formability, weather resistance and weldability.
Claims (1)
1. A high-strength high-plasticity ferrite-austenite dual-phase cold-rolled steel plate for automobiles is characterized by comprising the following chemical components in percentage by mass:
c: 0.2-0.4%, si is less than or equal to 0.1%, cu:1.0% -2.0%, mn: 6-8%, al: 0.4-0.8%, P <0.020%, S <0.006%, and the balance of Fe and inevitable impurities;
the production method of the high-strength high-plasticity ferritic-austenitic dual-phase cold-rolled steel plate for the automobile comprises the following steps of:
1) A heating process: heating the billet steel to 1000 +/-50 ℃ in a heating furnace, and preserving heat for 2 +/-0.5 hours;
2) The rolling process comprises the following steps: adopting common rolling and laminar cooling, wherein the final rolling temperature is 680 +/-30 ℃, and ensuring the coiling temperature to be 610 +/-30 ℃;
3) The cold rolling process comprises the following steps: the total cold rolling reduction is not lower than 60%;
4) Annealing process: annealing at 800 + -10 deg.C for 3 + -0.5 min, cooling at 25 + -5 deg.C/s to room temperature, keeping the temperature at 620-650 deg.C for 10 + -1.0 min, and furnace cooling to room temperature; the cold-rolled steel plate has the tensile strength of 980-1180MPa and the elongation of 30-35 percent.
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| CN100430505C (en) * | 2005-09-29 | 2008-11-05 | 宝山钢铁股份有限公司 | Superhigh-strength cold rolling band steel with anti-tensile strength above 880Mpa and its production |
| CN103805838B (en) * | 2012-11-15 | 2017-02-08 | 宝山钢铁股份有限公司 | High formability super strength cold-roll steel sheet and manufacture method thereof |
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| CN108546812B (en) * | 2018-05-14 | 2019-11-12 | 东北大学 | A kind of preparation method of high-strength medium managese steel plate |
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