CN114892073B - Steel plate suitable for cold spinning and manufacturing method thereof - Google Patents

Steel plate suitable for cold spinning and manufacturing method thereof Download PDF

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Publication number
CN114892073B
CN114892073B CN202210379117.XA CN202210379117A CN114892073B CN 114892073 B CN114892073 B CN 114892073B CN 202210379117 A CN202210379117 A CN 202210379117A CN 114892073 B CN114892073 B CN 114892073B
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steel plate
rolling
temperature
cold spinning
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CN114892073A (en
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白云
罗元东
孙宪进
苗丕峰
许峰
诸建阳
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Jiangyin Xingcheng Special Steel Works Co Ltd
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Jiangyin Xingcheng Special Steel Works 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
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
    • B21D22/14—Spinning
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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
    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0257—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment with diffusion of elements, e.g. decarburising, nitriding
    • 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
    • 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
    • C22C38/04—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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • 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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/20—Recycling

Abstract

The invention relates to a steel plate suitable for cold spinning and a manufacturing method thereof, wherein the chemical compositions of the steel plate are (by weight percent) C0.04-0.06, si 0.10-0.15, mn 1.30-1.50, al 0.02-0.04, nb 0.035-0.055, ti 0.01-0.02, S less than or equal to 0.0008, and [ H ]]≤1ppm，[O]Less than or equal to 8ppm, ca/S is more than or equal to 1.5; the balance being Fe and unavoidable impurities. The steel plate is a polygonal ferrite structure, the yield strength is more than or equal to 400MPa, the tensile strength is 450-550MPa, and the elongation A is the same as that of the steel plate 50 More than or equal to 50 percent, the yield ratio is less than or equal to 0.70, and the class-level sum of the A+B+C+D inclusions in the steel is less than or equal to 2.0; after cold spinning according to the compression ratio of 3.5-4 times and multi-pass spinning, the performance can meet the requirements that the yield strength is more than or equal to 600MPa, the tensile strength is more than or equal to 900MPa, and the elongation (A 50 ) Is more than or equal to 12 percent, and the surface is free from cracking.

Description

Steel plate suitable for cold spinning and manufacturing method thereof
Technical Field
The invention belongs to the technical field of iron-based metallurgy, and relates to a medium plate suitable for cold spinning mode processing and a manufacturing method thereof.
Background
In the field of mechanically manufacturing metal tubes, conventional manufacturing processes are to manufacture seamless steel tubes and medium plate bases first and then to weld the metal tubes. The process flow is long, the efficiency is low, the latest cold spinning production technology is adopted, the round cakes can be directly processed into the metal pipe barrel in a cold spinning processing mode, the integrated molding is realized, and the efficiency is greatly improved. The new technology puts very strict requirements on raw materials, not only requires the materials to have good cold processing performance and high elongation, but also requires the iron scale on the surfaces of the materials to be thin and uniform, the interior to be high-purity, and has no large-particle hard phase inclusion, and hard phase band-shaped tissues and internal stress which influence the processing performance.
At present, cold working steel plates are produced by adopting a mode of hot rolling steel coils and then carrying out acid washing treatment, and for the mode of directly adopting a medium plate to carry out cold spinning processing, the method is very rare, and series of problems such as the surface quality, the internal stress, the internal structure uniformity, the performance change before and after deformation and the like of the steel plates are required to be comprehensively evaluated.
Around the cold spinning process, developing a medium steel sheet that satisfies high uniform elongation, high performance uniformity and purity is a difficult problem that needs to be considered by those skilled in the art.
Disclosure of Invention
The invention aims to provide a medium steel plate capable of meeting cold spinning processing and a manufacturing method thereof.
The technical scheme adopted by the invention is as follows: a steel plate suitable for cold spinning processing comprises the following chemical components of 0.04-0.06 wt.% of C, 0.10-0.15 wt.% of Si, 1.30-1.50 wt.% of Mn, 0.02-0.04 wt.% of Al, 0.035-0.055 wt.% of Nb, 0.01-0.02 wt.% of Ti, less than or equal to 0.0008 wt.% of S, less than or equal to 1ppm of [ H ], [ O ]. Less than or equal to 8ppm, and more than or equal to 1.5 wt.% of Ca/S; the balance being Fe and unavoidable impurities.
The effect of key elements and the reason for setting the content of the key elements in the invention are specifically described as follows:
c: the key elements influencing the phase change in the steel have key influences on the strength and the elongation of the steel, and from the aspect of the elongation, the lower the carbon content is, the more favorable the improvement of the elongation, but the strength is greatly reduced; meanwhile, the excessive carbon content aggravates center segregation and has a great influence on tissue uniformity. The comprehensive balance is realized, and the content selection range of the C in the invention is 0.04-0.06%.
Si: the main deoxidizing element can play a role in solid solution strengthening, but has obvious influence on the surface quality of the steel plate, and the high silicon content easily causes that the iron scale is not removed cleanly in the descaling process, so that the surface quality is poor; comprehensively considering the surface requirements of the product in the patent of the invention, the Si content is selected to be 0.10-0.15%.
Mn: the main alloy strengthening elements in the invention improve the strength and toughness of steel through solid solution strengthening, but when the content is too high, a center segregation hardening zone is easily formed in the continuous casting process, and a brittle abnormal structure is generated, so that the stability of low-temperature toughness is not facilitated. The reasonable selection range of Mn in the invention is 1.30-1.50% by comprehensively considering the influence on low-temperature toughness and solid solution strengthening.
Al: the main deoxidizing element and the fine crystal element, and plays a role of refining grains by forming AlN. The Al content of the invention is selected to be 0.02-0.04%.
Nb: mainly refine grain elements, obviously improve the austenite recrystallization temperature of steel, enlarge the range of unrecrystallized areas, and obviously refine the prior austenite grain size; simultaneously forming fine Nb (C, N) precipitated phases when rolling in a non-recrystallization zone, and refining ferrite grains; considering together, the Nb content of the present invention is selected in the range of 0.035 to 0.055%.
Ti and N, C form TiN and TiC, so that the effect of refining the prior austenite crystal grains can be achieved, and the grain size of a welding heat affected zone can be refined due to the high melting point of TiN, so that the low-temperature toughness of the welding heat affected zone is improved. Comprehensively, ti is selected in the range of 0.01-0.02%.
S: harmful elements in steel are easy to form MnS hard phase inclusion with Mn, so that the elongation is not easy to be improved, meanwhile, the steel is easy to break in the cold spinning process, and the selection range of S is less than or equal to 0.0008% by comprehensive consideration;
h: the main influencing factors of delayed fracture in high-strength steel are that white spots are easily formed when the content is excessive, so that the elongation is reduced, brittle fracture occurs in the material, and for the cold spinning material, the strength is large in the final use state, so that the H content selection range is less than or equal to 1ppm;
o: the key index elements influencing the content of the inclusions are increased when the content of O is too high, so that the inclusions are easy to break in the spinning process, and the selection range of O is less than or equal to 8ppm by comprehensively considering;
ca promotes the inclusion to float up through Ca treatment, and simultaneously spheroidizes MnS, thereby improving the purity of molten steel and reducing the quality problem caused by internal defects in the spinning process. Comprehensively considering that the selection range of Ca is set according to the content of S, and Ca/S is more than or equal to 1.5.
Another object of the present application is to provide a method for manufacturing the above medium plate, with a thickness of 8-20mm, comprising the following process steps:
in the steelmaking process, a continuous casting blank with the thickness of 150mm is produced by adopting a converter smelting process, an RH+LF+RH vacuum degassing process, a calcium treatment process and a slab continuous casting process, and high-purity molten steel is obtained by adopting a double vacuum smelting process, a strict calcium treatment process and a soft argon blowing process, so that the molten steel is ensured to have no large-particle inclusion affecting cold spinning processing, mnS and other hard-phase inclusions;
meanwhile, a strict covering stacking slow cooling process is carried out on the continuous casting blank, the covering temperature is set to be 600-700 ℃, the covering time is 72 hours, and the covering temperature is set to be 100-200 ℃. The maximum diffusion of H is realized through a hood-added slow cooling process, and the occurrence probability of delayed cracks is reduced.
The continuous casting billet heating process comprises the following steps: the heating furnace is heated for 200-220min, the soaking section keeps the temperature 1180-1220 ℃, and the heat preservation time is more than or equal to 50min; by prolonging the heat preservation time of the high temperature section, the material homogenization is realized to the greatest extent, and the influence of the segregation zone on the cold spinning material is reduced. And after the heating furnace is discharged, the round trip high-pressure water descaling is carried out, so that the surface iron scale is ensured to be removed cleanly, and the influence of poor surface quality on the cold working process is reduced.
The rolling adopts a two-stage rolling process, wherein the first stage is a rough rolling stage, the austenite recrystallization zone is rolled, the initial rolling temperature is 1080-1150 ℃, the average rolling reduction rate of the last three times is more than or equal to 15 percent, the second stage is a finish rolling stage, the thickness of the finished steel plate is 2-2.5 times the thickness (mm) of the finished steel plate, the initial rolling temperature is 900-950 ℃, and the final rolling temperature is more than or equal to 800 ℃; and in the second stage of rolling, high-pressure water descaling is respectively carried out in the first pass, the second pass and the fourth pass, and the secondary iron scale is removed cleanly through three times of descaling.
After rolling, the steel plate is rapidly taken off line, the cover feeding temperature is more than or equal to 300 ℃, then cover adding and stacking slow cooling are carried out for more than 48 hours, then air cooling is carried out to room temperature, scratch on the surface is not allowed, and grinding is not allowed. The hydrogen diffusion treatment is further carried out by adding the cover to the steel plate for stacking and slow cooling, so that the H content in the steel plate is reduced, and the generation of delayed cracks after cold spinning is thoroughly eliminated.
For thin steel plates, the temperature drop speed is very high, the cover can be closed only by a cooling bed after finish rolling, the cover closing temperature of the common process is about 200 ℃, and the cover closing temperature is controlled to be more than or equal to 300 ℃.
After the steel plate manufactured by the production process is processed into a cake sample, the steel plate can meet the conditions that the yield strength is more than or equal to 600MPa, the tensile strength is more than or equal to 900MPa, the elongation A50 is more than or equal to 12 percent and the surface is free from cracking under the condition that the compression ratio before and after spinning is 3.5-4 under the multipass cold spinning process.
The cold spinning material capable of meeting the use requirements is obtained through the integrated design innovation of a component process system aiming at the characteristics of high homogeneity, high extension and no cracking required by the cold spinning material. In component design, the microstructure and performance of the base material are ensured through low-carbon low-manganese and Nb-Ti microalloying, the quantitative control requirement of harmful elements (S, H, O), particularly the control of O content, is highlighted, and the requirement of steel elements, particularly residual harmful elements, required by the cold spinning material can be accurately defined for the first time; and a specific manufacturing method is given in the manufacturing process. Secondly, in the aspect of tissue performance control, polygon ferritic steel with low residual stress is provided for the first time, the process for manufacturing the ultra-high strength steel plate with the strength of more than 600MPa by cold spinning is satisfied, verification is carried out in practice, and a specific control method is provided for specific processes required by obtaining the tissue.
Compared with the prior art, the invention has the advantages that:
aiming at the special requirements of the cold spinning material, the production of the medium plate which can meet the multi-pass cold spinning processing technology is realized by carrying out targeted design on the purity, the surface quality and the material performance of molten steel on the basis of reasonable component design, the structure of the medium plate before spinning is a low-stress high-homogeneity polygonal ferrite structure, the yield strength is more than or equal to 400MPa, and the tensile strength is 450-550MPa, elongation (A) 50 ) More than or equal to 50 percent, the yield ratio is less than or equal to 0.70, the sum of the levels of the A+B+C+D inclusion is less than or equal to 2.0, and after multi-pass spinning according to a cold spinning process with the compression ratio of 3.5 to 4 times, the performance can meet the conditions that the yield strength is more than or equal to 600MPa, the tensile strength is more than or equal to 900MPa, and the elongation (A 50 ) Is more than or equal to 12 percent, has no surface crack, and has impact energy of more than or equal to 230J at minus 60 ℃.
Drawings
FIG. 1 is a photograph of a microstructure of a low stress polygonal ferrite of a 10mm steel sheet according to an embodiment of the present invention.
Detailed Description
The present invention is described in further detail below in connection with the following examples, which are to be understood as being exemplary and not limiting of the technical solutions of the present application.
Examples 1-2:
according to the chemical composition range and the manufacturing method of the invention, medium steel plates which can be processed in a cold spinning processing mode can be manufactured through the process steps of converter smelting, RH vacuum decarburization, LF refining, RH vacuum degassing, calcium treatment, slab continuous casting, cover stack slow cooling, continuous casting blank checking and cleaning, casting blank heating, high-pressure water descaling, controlled rolling, cover stack slow cooling of steel plates and the like, wherein the cover-feeding casting blank temperature is 680 ℃ (example 1) and 670 ℃ (example 2).
The specific process of the heating, rolling and cooling stages is as follows: heating the continuous casting billet to 1180-1220 ℃, wherein the total heating time is 210min (example 1)/215 min (example 2), the soaking period heat preservation time is 52min (example 1) and 60min (example 2), and carrying out round trip descaling by using high-pressure water after the continuous casting billet is discharged from a furnace; then, controlled rolling is carried out, the initial rolling temperature in the rough rolling stage is 1080-1150 ℃ (examples 1 and 2), and the average rolling reduction of the last three times is 18% (example 1) and 20% (example 2); the thickness of the finish rolling to be warmed is 30mm (example 1)/25 mm (example 2), the initial rolling temperature of the finish rolling is 920-930 ℃ (example 1)/940-950 ℃ (example 2), the rolling reduction rate of the finish rolling accumulated pass is 60% (example 1)/60% (example 2), the final rolling temperature is 818 ℃ (example 1) and 804 ℃ (example 2), the final thickness of the finished steel plate is 12mm (example 1) and 10mm (example 2), the finished steel plate is rapidly cooled down after rolling in a piling way, the piling-up cooling cover-in temperature is 380 ℃ (example 1) and 330 ℃ (example 2), and the piling-up cooling is carried out for 48 hours (examples 1 and 2) and then the steel plate is cooled down to room temperature in a piling way.
The chemical compositions of the steel plates prepared in the examples are shown in table 1, the mechanical properties of the steel plates are shown in table 2, the mechanical properties of the steel plates after cold spinning are shown in table 3, and the microstructure of the steel plates is shown in fig. 1.
Table 1 chemical composition (wt.%) of the steel sheet of example
Examples C Si Mn Alt S Al Nb Ti H O Ca Ca/S
1-1 0.041 0.12 1.45 0.025 0.0006 0.024 0.041 0.015 0.00008 0.0007 0.0018 3
1-2 0.043 0.11 1.42 0.024 0.0005 0.025 0.040 0.014 0.00009 0.0008 0.0015 3
2-1 0.045 0.12 1.38 0.031 0.0007 0.028 0.042 0.015 0.00010 0.0008 0.0016 2.28
2-2 0.045 0.12 1.39 0.033 0.0004 0.028 0.043 0.015 0.00008 0.0006 0.0017 4.25
Table 2 mechanical properties of the steel sheets of examples
TABLE 3 mechanical Properties of the spun Material of the example Steel sheet
While the preferred embodiments of the present invention have been described in detail, it is to be clearly understood that the same may be varied in many ways by those skilled in the art. Any modification, equivalent replacement, improvement, etc. made within the spirit and principle of the present invention should be included in the protection scope of the present invention.

Claims (6)

1. A steel sheet suitable for cold spinning, characterized in that: the steel plate has chemical components of C0.04-0.06, si 0.10-0.15, mn 1.30-1.50, al 0.02-0.04, nb 0.035-0.055, ti 0.01-0.02, S less than or equal to 0.0008, H less than or equal to 1ppm, O less than or equal to 8ppm and Ca/S more than or equal to 1.5; the balance of Fe and unavoidable impurities;
the steel plate is a polygonal ferrite structure, the yield strength is more than or equal to 400MPa, the tensile strength is 450-550MPa, and the elongation A is the same as that of the steel plate 50 More than or equal to 50 percent, the yield ratio is less than or equal to 0.70, and the class-level sum of the A+B+C+D inclusions in the steel is less than or equal to 2.0; after cold spinning according to the compression ratio of 3.5-4 times and multi-pass spinning, the performance can meet the requirements that the yield strength is more than or equal to 600MPa, the tensile strength is more than or equal to 900MPa and the elongation A is more than or equal to 50 Is more than or equal to 12 percent, and the surface is free from cracking.
2. A method of manufacturing the steel sheet adapted for cold spinning according to claim 1, characterized in that: the process comprises the following steps:
(1) smelting raw materials sequentially pass through converter top-bottom blowing, RH vacuum degassing, LF refining, RH vacuum degassing and calcium treatment, casting to obtain casting blanks with the thickness of 150mm and above, and the center segregation of the casting blanks meets the C0.5 level requirement; adding a cover for stacking and slowly cooling a casting blank;
(2) heating a casting blank: heating and preserving heat of the casting blank in a heating furnace to ensure that the structure is completely austenitized, alloy elements are fully dissolved in solid, the structure is homogenized, and carrying out round trip high-pressure water descaling for two times after discharging, so as to remove oxide skin on the surface of the casting blank;
(3) rolling: adopting two-stage rolling, wherein the first stage is a rough rolling stage, the austenite recrystallization zone rolling is carried out, the initial rolling temperature is 1080-1150 ℃, and the average rolling reduction rate of the last three times is more than or equal to 15%; the second stage is a finish rolling stage, wherein the thickness of a finished steel plate with the temperature to be 2-2.5 times of the thickness of the finished steel plate is 900-950 ℃ in the initial rolling temperature, and the final rolling temperature is more than or equal to 800 ℃; in the second stage of rolling, high-pressure water descaling is respectively carried out in the first several passes;
(4) and (3) adding a cover to the rolled steel plate, carrying out stack slow cooling, wherein the cover feeding temperature is more than or equal to 300 ℃, and carrying out air cooling to room temperature after stack slow cooling, wherein scratch is not allowed on the surface, and coping and shot blasting are not allowed.
3. The method for manufacturing a steel sheet suitable for cold spinning according to claim 2, wherein: the casting blank cover entering temperature of the step (1) is 600-700 ℃, the cover adding time is more than 72 hours, and the cover exiting temperature is 100-200 ℃.
4. The method for manufacturing a steel sheet suitable for cold spinning according to claim 2, wherein: the soaking section heat preservation temperature in the step (2) is 1180-1220 ℃, and the soaking section heat preservation time is more than or equal to 50min.
5. The method for manufacturing a steel sheet suitable for cold spinning according to claim 2, wherein: and (3) in the finish rolling stage, the surface of the steel billet is descaled in the first pass, the second pass and the fourth pass respectively.
6. The method for manufacturing a steel sheet suitable for cold spinning according to claim 2, wherein: and (3) covering the rolled steel plate for slow cooling for more than 48 hours.
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