CN113151651B - Production method of low-temperature annealed ultra-deep drawn cold-rolled steel plate and cold-rolled steel plate - Google Patents
Production method of low-temperature annealed ultra-deep drawn cold-rolled steel plate and cold-rolled steel plate Download PDFInfo
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- CN113151651B CN113151651B CN202011026937.8A CN202011026937A CN113151651B CN 113151651 B CN113151651 B CN 113151651B CN 202011026937 A CN202011026937 A CN 202011026937A CN 113151651 B CN113151651 B CN 113151651B
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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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing 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
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0426—Hot rolling
-
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0436—Cold rolling
-
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
Abstract
The invention discloses a production method of a low-temperature annealing ultra-deep drawing cold-rolled steel plate, which comprises the following steps: controlling the components of the steel plate according to the weight percentage, and continuously casting the components after smelting into a continuous casting blank; heating the casting blank to 1190-1220 ℃, and then sequentially carrying out rough rolling and finish rolling to obtain a hot rolled plate with the thickness of 3-6 mm; after finish rolling, cooling to 590-620 ℃ in a front-section cooling laminar cooling mode, and coiling to obtain a hot-rolled coil; uncoiling the hot-rolled coil, cleaning and then carrying out cold rolling to obtain strip steel; annealing the strip steel in a continuous annealing furnace; and cooling the continuously annealed strip steel to room temperature through a flume, and performing finishing. The temperature in the production process is controlled to realize good mechanical property of the finished product, and the steel plate with low yield strength and high elongation is obtained. The invention also discloses a low-temperature annealing ultra-deep drawing cold-rolled steel plate produced by using the production method.
Description
Technical Field
The invention belongs to the technical field of steel rolling, and particularly relates to a production method of a low-temperature annealing ultra-deep drawing cold-rolled steel plate and the low-temperature annealing ultra-deep drawing cold-rolled steel plate produced by the method.
Background
With the continuous development of the automobile industry, the requirement of the market on the board for the household appliances is continuously improved, and the stamping forming performance is gradually improved on the premise of ensuring the performance. Good stamping properties require steel sheets with lower yield strength and higher elongation. In the prior art, the mechanical property requirements of the steel plate are usually met by adopting deep decarburization, alloy element addition and other modes, but the production cost of the steel plate is undoubtedly increased.
Disclosure of Invention
In order to solve the technical problems in the prior art, the invention provides a production method of a low-temperature annealing ultra-deep drawing cold-rolled steel plate, which realizes good mechanical property of a finished product by controlling the temperature in the production process and obtains a steel plate with low yield strength and high elongation. The invention also discloses a low-temperature annealing ultra-deep drawing cold-rolled steel plate produced by using the production method.
According to the invention, the production method of the low-temperature annealing ultra-deep drawing cold-rolled steel plate comprises the following steps:
casting blank: controlling the components of the steel plate according to the weight percentage: c: 0.0001 to 0.005%, Si: 0.001 to 0.03%, Mn: 0.03-0.09%, P: 0.005-0.015%, S: 0.008-0.015%, Ti: 0.055-0.080%, Als: 0.020-0.070 percent, and the balance of Fe and inevitable impurities, and continuously casting the components after smelting into a continuous casting blank;
hot rolling: heating the casting blank to 1190-1220 ℃, and then sequentially carrying out rough rolling and finish rolling to obtain a hot rolled plate with the thickness of 3-6 mm, wherein the start rolling temperature of the finish rolling is controlled to be 1020-1070 ℃, and the finish rolling temperature is controlled to be 910-940 ℃;
coiling: after finish rolling, cooling to 590-620 ℃ in a front-section cooling laminar cooling mode, and coiling to obtain a hot-rolled coil;
cold rolling: uncoiling the hot-rolled coil, cleaning and then carrying out cold rolling to obtain strip steel;
and (3) continuous annealing: annealing the strip steel in a continuous annealing furnace, wherein the temperature of the strip steel in a soaking section is controlled to be 760-790 ℃, and the temperatures of the strip steel at a slow cooling terminal and a fast cooling terminal of the continuous annealing furnace are respectively controlled to be 670-700 ℃ and 430-450 ℃;
finishing: and cooling the continuously annealed strip steel to room temperature through a flume, and finishing.
According to one embodiment of the invention, smelting comprises molten iron desulphurization, converter smelting, LF furnace Ca treatment and RH decarburization.
According to one embodiment of the invention, the furnace time before the rough rolling of the casting blank is 200-300 min.
According to one embodiment of the invention, the rough rolling of the casting blank adopts 5-pass rolling, wherein the phosphorus is removed in the whole number of the 5-pass rolling.
According to one embodiment of the invention, the thickness of the intermediate slab after rough rolling of the cast slab is 38mm to 45 mm.
According to one embodiment of the invention, the cold rolling reduction is 70% to 85%.
According to one embodiment of the invention, the unit speed of the strip steel in the continuous annealing furnace is 220-320 m/min.
According to one embodiment of the invention, the temperature of the steel strip at the end of overaging in the continuous annealing process is controlled at 400-430 ℃.
According to an embodiment of the present invention, the finishing elongation is controlled to be 0.6-1.0%.
According to the present invention, there is provided a low-temperature annealed ultra-deep drawn cold rolled steel sheet produced using the above production method.
Due to the adoption of the technical scheme, compared with the prior art, the invention has the following advantages: by controlling the key process temperature of the hot rolling, cold rolling and annealing processes, the mechanical properties of yield strength of 130-160MPa, tensile strength of 270-310 MPa, elongation of more than or equal to 44.0%, r90 (plastic strain ratio) of more than or equal to 2.5 and n90 (strain hardening index) of more than or equal to 0.22 are obtained, the requirements of low yield strength and high elongation are met, and low-energy-consumption production is realized. In addition, other special procedures are not introduced according to the method of the invention, which is beneficial to popularization and application in the existing cold rolling continuous annealing production lines at home and abroad.
Detailed Description
In order to make the objects, technical solutions and advantages of the present invention more apparent, the present invention is further described in detail with reference to the following embodiments. It should be understood that the specific embodiments described herein are merely illustrative of the invention and are not intended to limit the invention.
The production method of the low-temperature annealing ultra-deep drawing cold-rolled steel plate generally comprises the steps of casting blanks, heating steel blanks to a temperature higher than the recrystallization temperature for hot rolling, cooling and coiling the hot-rolled steel blanks into coils, uncoiling, cleaning and cold rolling to obtain strip steel, and finally continuously annealing and finishing the strip steel to obtain finished steel plates. Specifically, the mechanical properties of the finished steel plate 1 meet the requirements of yield strength of 130-160MPa, tensile strength of 270-310 MPa, elongation of 44.0% or more, r90 of 2.5 or more, and n90 of 0.22 or more by controlling the temperature of each step in the hot rolling and annealing treatment and controlling other related parameters.
Casting blank
Controlling the components of the steel plate according to the weight percentage: c: 0.0001 to 0.005%, Si: 0.001 to 0.03%, Mn: 0.03-0.09%, P: 0.005-0.015%, S: 0.008-0.015%, Ti: 0.055-0.080%, Als: 0.020-0.070 percent, and the balance of Fe and inevitable impurities, and continuously casting the components after smelting into a continuous casting blank. Wherein, the smelting process can comprise the working procedures of molten iron desulphurization, converter smelting, LF (ladle refining) furnace Ca treatment, RH (vacuum) decarburization and the like.
The reasons for selecting the chemical components and their ranges in the present invention are as follows: the selection of the carbon content range mainly considers the matching of strength, formability and welding performance, if the carbon content is lower than 0.010 percent, the strength of the steel plate is low, and decarburization is needed in the production process; if it is higher than 0.010%, formability and weldability of the steel sheet are deteriorated, and the performance control at low strength level is not facilitated. Silicon: si can be dissolved in ferrite and austenite to improve the strength of the steel, and the action of Si is second to C, P, Si, so that the precipitation of carbide in the ferrite can be inhibited, solid solution C atoms are fully enriched in the austenite, and the stability of the steel is improved. However, when the content of Si is too high, the surface iron scale formed in the heating furnace by Si is difficult to remove, and the dephosphorization difficulty is increased. Therefore, the Si content of the present invention is less than 0.30%. Mn is mainly in a solid solution strengthening mode to improve the strength and is combined with sulfur to form MnS, thereby preventing hot cracking caused by FeS, and the welding performance of steel is influenced due to the excessively high Mn content. S exists as residual element, and is controlled to be less than or equal to 0.018 percent. Aluminum is mainly added as a deoxidizing element, the content of the aluminum is required to be more than 0.010 percent to realize complete deoxidation, but the excessive aluminum influences the welding performance of steel and the control of casting blank inclusions, so the content of the aluminum is preferably selected to be 0.010 to 0.070 percent. The microalloy Ti is added to combine with C, N element to form Ti (C, N), and clearance atoms are removed to obtain a pure ferrite matrix. The Ti content is low, interstitial atoms cannot be completely removed, the strength can be obviously improved due to the excessively high Ti content, the service performance is influenced, and the punched part can be seriously cracked. Therefore, the Ti content is preferably 0.055% to 0.080%.
The chemical compositions and ranges of the cold rolled steel sheets of the specific examples 1 to 8 and the comparative examples 1 to 2 are shown in Table 1:
TABLE 1 Cold rolled steel sheet chemical composition (wt.%)
Hot rolling
Heating the casting blank to 1190-1220 ℃, and then sequentially carrying out rough rolling and finish rolling to obtain a hot rolled plate with the thickness of 3-6 mm. Wherein the start rolling temperature of finish rolling is controlled to be 1020-1070 ℃, and the finish rolling temperature range is controlled to be 910-940 ℃. The finish rolling is carried out in an austenite region close to Ar3 (the temperature at which austenite transforms into ferrite), so that fine structures can be obtained by hot rolling.
In the embodiment of the invention, the furnace time before the rough rolling of the casting blank is 200-300 min, so that the integral temperature of the casting blank can be ensured to be uniform, and the oversize of crystal grains in the casting blank can be avoided. And 5-pass rolling is adopted for rough rolling, wherein the total phosphorus is removed by the 5-pass rolling, and an intermediate plate blank with the thickness of 38-45 mm is obtained after the casting blank is roughly rolled.
The main process parameters of hot rolling of the specific examples 1 to 8 and the comparative examples 1 to 2 are shown in Table 2:
TABLE 2 Hot Rolling Main Process parameters
Coiling and cold rolling
And after finish rolling, cooling to 590-620 ℃ in a front-stage cooling laminar cooling mode, and coiling to obtain a hot-rolled coil. The hot rolled coil is subsequently uncoiled, cleaned, for example pickled, and then cold rolled to obtain a strip. Wherein the reduction rate is determined to be 70-85% by combining the capacity of a cold rolling mill.
The main process parameters for coiling and cold rolling of specific examples 1-8 and comparative examples 1-2 are shown in Table 3:
TABLE 3 Main Process parameters for coiling and Cold Rolling
| Number of | Coiling temperature/. degree.C | Cold rolling reduction/%) |
| Set range | 590～620 | 70-85 |
| Example 1 | 601 | 80 |
| Example 2 | 597 | 80 |
| Example 3 | 605 | 72 |
| Example 4 | 590 | 80 |
| Example 5 | 611 | 75 |
| Example 6 | 620 | 81 |
| Example 7 | 609 | 85 |
| Example 8 | 600 | 80 |
| Comparative example 1 | 751 | 80 |
| Comparative example 2 | 747 | 80 |
Continuous annealing and finishing
Annealing the strip steel in a continuous annealing furnace, wherein the temperature of the strip steel in a soaking section is controlled to be 760-790 ℃, and the temperatures of the strip steel at a slow cooling terminal point, a fast cooling terminal point and an effect ending terminal point of the continuous annealing furnace are respectively controlled to be 670-700 ℃, 430-450 ℃ and 400-430 ℃. In the embodiment of the invention, the unit speed of the strip steel in the continuous annealing furnace can be controlled to be 220-320 m/min.
And cooling the continuously annealed strip steel to room temperature through a flume, and performing finishing. Wherein, the finishing elongation can be controlled to be 0.6-1.0%.
The main process parameters for continuous annealing and finishing of the specific examples 1-8 and comparative examples 1-2 are shown in Table 4:
TABLE 4 continuous annealing and finishing Main Process parameters
The mechanical properties of the cold rolled steel sheets produced using the methods of specific examples 1 to 8 and comparative examples 1 to 2 are shown in Table 5:
TABLE 5 mechanical Properties of Cold-rolled Steel sheets
| Numbering | Thickness/mm | Rp0.2/MPa | Rm/MPa | Elongation A80/％ | n90 | r90 |
| Performance requirements | 0.6 | 130-160 | 270～310 | ≥44.0％ | ≥0.22 | ≥2.5 |
| Example 1 | 0.6 | 147 | 301 | 45.5 | 0.23 | 2.7 |
| Example 2 | 0.6 | 147 | 301 | 46.0 | 0.23 | 2.7 |
| Example 3 | 0.7 | 146 | 303 | 45.5 | 0.23 | 2.7 |
| Example 4 | 0.6 | 145 | 302 | 46.5 | 0.23 | 2.6 |
| Example 5 | 1.5 | 146 | 305 | 46.5 | 0.23 | 2.7 |
| Example 6 | 0.6 | 148 | 305 | 45.5 | 0.23 | 2.7 |
| Example 7 | 0.6 | 152 | 310 | 44.5 | 0.23 | 2.6 |
| Example 8 | 0.6 | 149 | 302 | 45.5 | 0.23 | 2.7 |
| Comparative example 1 | 0.6 | 149 | 289 | 43.5 | 0.22 | 2.5 |
| Comparative example 2 | 0.6 | 150 | 297 | 43.0 | 0.22 | 2.4 |
As can be seen from the mechanical properties shown in table 5, the cold-rolled steel sheets produced using the methods according to examples 1 to 8 of the present invention effectively improved the elongation while maintaining the low yield strength, and further improved the press formability of the entire steel sheet, as compared to the comparative example.
The above examples only express embodiments of the present invention, and the description thereof is more specific and detailed, but not construed as limiting the scope of the present invention. It should be noted that, for a person skilled in the art, several variations and modifications can be made without departing from the inventive concept, which falls within the scope of the present invention. Therefore, the protection scope of the present patent shall be subject to the appended claims.
Claims (9)
1. The production method of the low-temperature annealing ultra-deep drawing cold-rolled steel plate is characterized by comprising the following steps of:
casting blank: controlling the components of the steel plate according to the weight percentage: c: 0.0001 to 0.005%, Si: 0.001 to 0.03%, Mn: 0.03-0.09%, P: 0.005-0.015%, S: 0.008-0.015%, Ti: 0.055-0.080%, Als: 0.020-0.070%, and the balance of Fe and inevitable impurities, and continuously casting the components after smelting into a continuous casting blank;
hot rolling: heating the casting blank to 1190-1220 ℃, and then sequentially carrying out rough rolling and finish rolling to obtain a hot rolled plate with the thickness of 3-6 mm, wherein the start rolling temperature of the finish rolling is controlled to be 1020-1070 ℃, the final rolling temperature range is 910-940 ℃, and the rough rolling of the casting blank adopts 5-pass rolling;
coiling: after finish rolling, cooling to 590-620 ℃ in a front-section cooling laminar cooling mode, and coiling to obtain a hot-rolled coil;
cold rolling: uncoiling a hot-rolled coil, cleaning, and then carrying out cold rolling to obtain strip steel, wherein the cold rolling reduction rate is 70-85%;
and (3) continuous annealing: annealing the strip steel in a continuous annealing furnace, wherein the temperature of the strip steel in a soaking section is controlled to be 760-790 ℃, and the temperatures of the strip steel at a slow cooling terminal and a fast cooling terminal of the continuous annealing furnace are respectively controlled to be 670-700 ℃ and 430-450 ℃;
finishing: and cooling the continuously annealed strip steel to room temperature through a flume, and performing finishing.
2. The production method according to claim 1, wherein the smelting includes molten iron desulfurization, converter smelting, LF furnace Ca treatment, and RH decarburization.
3. The production method according to claim 1, wherein the furnace time before rough rolling of the cast slab is 200 to 300 min.
4. The production method of claim 1, wherein the phosphorus is removed by rolling in 5 passes.
5. The production method according to claim 1, wherein the thickness of the intermediate slab after the rough rolling of the cast slab is 38mm to 45 mm.
6. The production method according to claim 1, wherein the unit speed of the strip steel in the continuous annealing furnace is 220 to 320 m/min.
7. The production method as claimed in claim 1, wherein the temperature of the strip at the end of the overaging in the continuous annealing process is controlled to 400-430 ℃.
8. The production method according to claim 1, wherein the finishing elongation is controlled to be 0.6 to 1.0%.
9. A low-temperature annealed ultra-deep drawn cold rolled steel sheet produced using the production method as set forth in any one of claims 1 to 8.
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| CN104745935A (en) * | 2015-03-26 | 2015-07-01 | 攀钢集团西昌钢钒有限公司 | Production method for cold-rolled steel sheet with excellent stamping property |
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| CN104611535A (en) * | 2015-02-06 | 2015-05-13 | 攀钢集团攀枝花钢铁研究院有限公司 | Cold-rolled steel sheet and preparation method thereof |
| CN104694817B (en) * | 2015-03-26 | 2016-11-09 | 攀钢集团西昌钢钒有限公司 | Ultralow carbon cold-rolled steel plate production method |
| CN110592348A (en) * | 2019-09-27 | 2019-12-20 | 攀钢集团攀枝花钢铁研究院有限公司 | Ultra-low carbon cold rolled steel performance grading control method |
| RU2721263C1 (en) * | 2019-12-23 | 2020-05-18 | Федеральное Государственное Унитарное Предприятие "Центральный научно-исследовательский институт черной металлургии им. И.П. Бардина" (ФГУП "ЦНИИчермет им. И.П. Бардина") | Method for production of cold-rolled annealed rolled products from if-steel |
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