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CN108796363B - High-surface-quality aluminum-coated substrate steel suitable for large deformation and stamping and production method thereof - Google Patents

High-surface-quality aluminum-coated substrate steel suitable for large deformation and stamping and production method thereof Download PDF

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CN108796363B
CN108796363B CN201710287034.7A CN201710287034A CN108796363B CN 108796363 B CN108796363 B CN 108796363B CN 201710287034 A CN201710287034 A CN 201710287034A CN 108796363 B CN108796363 B CN 108796363B
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aluminum
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CN108796363A (en
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宋凤明
王巍
胡晓萍
杨阿娜
李建业
张华�
杜巍星
王天柱
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Baoshan Iron and Steel Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • 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
    • C21D2211/002—Bainite
    • 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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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

The steel for the high-surface-quality aluminum-coated substrate, which is suitable for large deformation and stamping processing, and the production method thereof comprise the following chemical components in percentage by weight: c is less than or equal to 0.01 percent, Si: 0.006-0.015%, Mn: 0.05-0.3%, P is less than or equal to 0.015%, S is less than or equal to 0.01%, Al is less than or equal to 0.005%, N is less than or equal to 0.005%, Ti: 0-0.05%, O: 0.01-0.08%, and the balance of Fe and inevitable impurities; and, simultaneously: c + N is less than or equal to 0.012; Mn/S is more than or equal to 8; Ti/(3.42N +4C) ≥ 1. The tensile strength of the steel for the aluminum-clad substrate is 280-380MPa, and the elongation is more than 40%; the low-C-Si-Mn alloy with the components similar to pure iron is designed, a proper amount of Ti is added, the production is carried out by adopting a controlled rolling mode, the production process is simple, and the cost is lower. The steel has excellent plasticity and steel-aluminum combination performance, meets the requirement of single-pass large deformation (80-90 percent), and is mainly used for producing aluminum-clad plate strips.

Description

High-surface-quality aluminum-coated substrate steel suitable for large deformation and stamping and production method thereof
Technical Field
The invention belongs to the field of manufacturing of ultra-low carbon steel, and particularly relates to high-surface-quality steel for an aluminum-coated substrate, which is suitable for large deformation and stamping processing, and a production method thereof.
Background
With the development of technology and economy, the performance requirements on metal materials are higher and higher, and the metal materials with single composition are often difficult to meet the requirements of multi-aspect performance in the actual use process. The composite board is made of two or more metal materials by various different processes, and can meet the special comprehensive performance requirements. The aluminum-clad steel is a composite plate strip which is formed by cladding an aluminum film on the surface of a strip steel by rolling at room temperature to form a surface aluminum layer and a core layer steel layer, has the strength of the existing steel, and has the characteristics of good heat dissipation, corrosion resistance, portability and attractive appearance of aluminum, and particularly greatly reduces the cost. The aluminum-clad plate applied to the fields of household electrical panels, automobile parts, food processing trays and the like is required to have good steel-aluminum bonding strength, excellent stamping performance and high surface quality, particularly the latter two requirements, and the current aluminum-clad product is difficult to meet.
Chinese patent No. CN102019727 discloses an "aluminum-coated steel strip for a cooler and a preparation method thereof and a steel strip and an aluminum alloy strip used thereby", which introduces a method and a process for producing a composite strip, and although referring to a substrate used therein, it is mainly used for producing a thicker aluminum-coated steel strip, and has insufficient plastic deformation capability, difficulty in meeting the requirement of large deformation (deformation not more than 70%), and poor surface quality.
The substrate used for producing the aluminum-clad steel strip is deformed together with the aluminum film on the surface in the production process of the composite strip, so that the substrate is required to have strength and plasticity equivalent to those of aluminum, and is generally low in strength and excellent in plasticity. However, the aluminum-clad substrate also requires good steel-aluminum lamination performance, so that the common low-strength steel is difficult to be used for aluminum-clad steel production.
Japanese patent No. JP2005281806 discloses a low yield point steel with excellent toughness and a production method thereof, belonging to a low alloy structural steel with lower yield strength and higher elongation, and the yield strength is generally about 200 MPa. These patents are generally thick plate products, and are mainly used for the production of anti-seismic dampers, in which one or more components of chromium (Cr), molybdenum (Mo), nickel (Ni), copper (Cu), boron (B) and other alloys are added on the basis of lower carbon (C) -silicon (Si) -manganese (Mn) in the component design.
Chinese patent publication No. CN101775535A discloses a 160 MPa-grade anti-seismic low-yield-point steel, a steel plate and a manufacturing method thereof, which relates to the fact that the steel is a thick plate product and is mainly used for manufacturing an anti-seismic damper and does not have good steel-aluminum composite performance, while the invention relates to the fact that the steel is mainly used for producing aluminum-coated strip steel and requires low yield strength, good plasticity and good steel-aluminum interface bonding performance, high surface quality and stamping performance.
In addition, chinese patent publication No. CN101525720 in 2009 discloses a "novel special matrix steel strip for producing an aluminum-coated steel strip", which relates to a steel type with a high alloy content, wherein the Mn content is 15-30%, and the matrix steel strip deformation amount is about 50% in terms of rolling deformation.
Compared with the prior patent, the single-pass deformation of the prior aluminum-coated steel product is generally below 70 percent, and the surface has the problems of uneven strain, strip-shaped stripes and incapability of stamping; the low yield point steel has excellent plasticity and large deformability, but the steel-aluminum combination property is poor, so that the steel-aluminum combination processing cannot be carried out.
The invention content is as follows:
the invention aims to provide the steel for the high-surface-quality aluminum-coated substrate, which is suitable for large deformation and stamping processing, and the production method thereof, wherein the tensile strength is 280-380MPa, and the elongation is more than 40%; besides good plasticity and steel-aluminum lamination performance, the aluminum clad plate strip can meet the requirement of single-pass large deformation (80-90%), and the aluminum clad plate strip produced by using the aluminum clad plate strip as a base plate has good surface quality and no macroscopic stripe defect on the surface of the plate strip.
In order to achieve the purpose, the technical scheme of the invention is as follows:
the steel of the invention is designed by low C-Si-Mn similar to pure iron and is added with proper amount of Ti, and is produced by adopting a controlled rolling mode,
specifically, the steel for the high-surface-quality aluminum-coated substrate, which is suitable for large deformation and stamping processing, comprises the following chemical components in percentage by weight: c is less than or equal to 0.01 percent, Si: 0.006-0.015%, Mn: 0.05-0.3%, P is less than or equal to 0.015%, S is less than or equal to 0.01%, Al is less than or equal to 0.005%, N is less than or equal to 0.005%, Ti: 0-0.05%, O: 0.01-0.08%, and the balance of Fe and inevitable impurities; and, simultaneously:
C+N≤0.012；
Mn/S≥8；
Ti/(3.42N+4C)≥1。
the microstructure of the steel of the present invention is a uniform equiaxed ferrite structure and a small amount of bainite structure. The tensile strength of the steel is 280-380MPa, and the elongation is more than 40%.
The strength of a steel sheet is generally improved by means of solid solution strengthening, precipitation strengthening, dislocation strengthening, grain boundary strengthening, and the like. The aluminum-clad substrate disclosed by the invention has the advantages of tensile strength of 280-380MPa, elongation of more than 40%, and good steel-aluminum bonding performance and stamping performance. The content of the specific alloy elements must be limited as much as possible. The reasons for defining the specific chemical composition are as follows:
c, the yield strength is increased and the elongation is reduced through solid solution strengthening; meanwhile, higher C is easy to be partially polymerized at defect positions such as dislocation and the like, and is unfavorable for surface quality. According to the actual steel-making process, the content of the steel should be reduced as much as possible, and 0.01 percent is an upper limit.
Si is a deoxidizing element and a solid solution strengthening element, so that the yield strength is improved, the elongation is reduced, and the proper Si is beneficial to improving the interface bonding performance of steel and aluminum, so that the addition amount of Si is controlled to be 0.006-0.015%.
Mn is also a common strengthening element in steel, and the yield strength is improved through solid solution strengthening, so that the elongation is reduced; however, an appropriate amount of Mn can combine with S in the steel to form MnS, which reduces the hot brittleness of the steel, but too high Mn content prevents recovery and suppresses the growth of recrystallized grains, and lowers the strength of the gamma texture (ND/111), which is very disadvantageous for press forming of steel sheets, so that the content is controlled to 0.05-0.3%.
The higher P causes cold brittleness of the steel, reduces plasticity and impact toughness, deteriorates welding performance and cold bending performance of the steel, and is unfavorable for steel-aluminum interface bonding, so the content of P in the steel is reduced as much as possible, and the content is required to be controlled below 0.015 percent in the invention.
S is unfavorable to the performance of steel, is easy to cause the hot brittleness of the steel, reduces the low-temperature toughness of the steel and deteriorates the bonding performance of a steel-aluminum interface. Mn can be added to form MnS together with S, the hot ductility can be improved by increasing the Mn/S ratio, the S content is required to be controlled to be less than 0.01 percent, and the Mn/S ratio is limited to be more than or equal to 8.
Al is an important deoxidizing element of steel, but high Al is easy to diffuse to a steel-aluminum bonding interface, and the bonding strength of the interface is deteriorated. Therefore, the content thereof must be controlled within a certain range, and the upper limit of the content is required to be 0.005% in the present invention.
N can form AlN particles with Al in steel so as to inhibit the diffusion of Al to an interface, but N is similar to C and is easy to form Coriolis gas masses at dislocation positions to be unfavorable for the subsequent surface quality, so the upper limit of the content of N is controlled to be 0.005 percent, and C + N is less than or equal to 0.012 percent.
Ti is used to fix C, N atoms to reduce their effect of hindering dislocation movement, and Ti can form TiN → Ti in sequence in steel4C2S2→ TiS and TiC, free C, N atoms in the steel are eliminated, and the formation of Cochler's gas clusters is reduced, which is beneficial to improving the surface quality. However, since a large amount of Ti lowers the elongation of the steel sheet, the amount of Ti to be added is limited to 0.05% or less. Meanwhile, the content of C, N, Ti is limited to satisfy the relation Ti/(3.42N +4C) ≥ 1.0.
Oxygen (O) element can suppress adverse effects of Al element in steel on steel-aluminum interface bonding, so that it is required to appropriately add a certain content of O element. In the present invention, the contents of Si and Al are limited to extremely low ranges, so that the oxygen content in the steel is inevitably high. However, too high oxygen can cause defects such as subcutaneous bubbles, porosity, etc., and exacerbate the hot brittle effect of sulfur. During the solidification of the steel, oxygen is precipitated in a large amount in the form of oxides, and the plasticity, impact toughness, and other workability of the steel are reduced. Therefore, the content is limited to 0.01 to 0.08%.
The invention relates to steel grade, which is required to have excellent plasticity to meet the requirements of aluminum-clad rolling and meet the requirements of single-pass large deformation, stamping and high surface quality on the basis of good steel-aluminum combination performance. By controlling the C, N content in the steel to be less than 0.005 percent, the strength of the substrate and the segregation of interstitial atoms at dislocation positions are adjusted, the problem of uneven surface deformation is solved, the surface quality is improved, and the stamping performance is ensured; the distribution of C, N atoms in the grain boundary is further limited by the addition of Ti, which is beneficial to the improvement of the stamping performance; meanwhile, the components of Si, Al and O are controlled in a specific range, so that the steel grade has excellent steel-aluminum combination performance. The P, S component control is beneficial to obtaining a billet with excellent inner quality, improving the steel-aluminum combination property, low-temperature toughness and the like of the steel plate, and the limit of 0.05-0.3 percent of Mn component is beneficial to the aluminum coating property. In general, with the above-described required component system, an invention steel grade satisfying the requirements can be obtained.
The invention relates to a method for producing high-surface-quality steel for an aluminum-clad substrate, which is suitable for large deformation and stamping processing, and comprises the following steps of,
1) smelting
Pretreating molten iron, blowing the converter top and bottom, refining outside the furnace, and continuously casting to form a plate blank;
2) reheating the plate blank, wherein the heating temperature is 1180-1220 ℃;
3) controlled rolling
Two-stage controlled rolling is adopted, the finish temperature of rough rolling is over 980 ℃, and the accumulated deformation in the rough rolling stage is more than or equal to 80 percent; the inlet temperature of finish rolling is above 950 ℃, and the finish rolling finishing temperature is 820-860 ℃;
4) controlling cooling at a water cooling speed of more than 10 ℃/s;
5) and (4) coiling at the coiling temperature of 540-600 ℃.
In the production process of the invention:
pretreating molten iron, removing P, S, and ensuring the low P, S content in steel; and (4) carrying out composite blowing at the top and the bottom of the converter, and controlling the content of C.
Considering the dissolution behavior of the microalloy element carbonitride in austenite and the growth behavior of austenite grains in the heating process, the invention requires that the casting blank is reheated at 1180-1220 ℃, and a two-stage controlled rolling process is adopted. Controlling the finish temperature of rough rolling to be over 980 ℃, the finish rolling inlet temperature to be over 950 ℃, the finish rolling end temperature to be between 820 and 860 ℃, the coiling temperature to be within the range of 540 to 600 ℃, and the water cooling speed to be over 10 ℃/s.
From the continuous cooling curve of fig. 1, the ferrite transformation temperature of the steel grade is approximately 890 ℃. The finish rolling finishing temperature is controlled to be 820-860 ℃, so that finish rolling in a ferrite area can be guaranteed to be finished, and good plate shape and expected structure and performance are obtained; the steel strip is too high and easily enters an austenite phase region and a ferrite phase region, mixed crystals are easily formed in a matrix, and rolling force fluctuation is caused at the same time, so that the steel strip is unfavorable for thickness control and strip shape; if the temperature is too low, the heat distortion resistance is increased, and the rolling load is increased, so that the energy consumption is increased.
According to the start temperature of finish rolling, the inlet temperature of finish rolling is controlled to be more than 950 ℃ and the finish temperature of rough rolling is controlled to be more than 980 ℃ according to corresponding requirements. From the CCT curve, the present invention relates to steel grades having a wide ferrite region. In order to realize the target performance and ensure the effect of recrystallizing and refining grains, the accumulated deformation amount in the rough rolling stage is required to be more than or equal to 80 percent.
In order to obtain good surface quality of the strip steel, the side pressure in the rough rolling stage is controlled within 50 mm. Meanwhile, the corner position of the casting blank is required to have no defects of air holes, scars and the like, or the surface of the casting blank is required to be cleaned.
In order to obtain the required properties, the matrix structure of the steel is required to be controlled to be equiaxed ferrite and a small amount of bainite. As can be seen from the continuous cooling curve, ferrite + bainite structures can be obtained at cooling rates of 10 ℃/s or more. Considering rapid cooling to refine the structure and the time for completion of transformation, in order to complete most of ferrite → bainite transformation in a short time while avoiding formation of pearlite structure, the cooling rate must be controlled to 10 ℃/s or more. Therefore, the cooling speed of the steel grade after rolling is controlled to be more than 10 ℃/s.
The coiling temperature is determined according to the phase transformation point of the steel and combined with the target structure. As seen in fig. 1, the martensitic transformation starting temperature of the steel is about 535 ℃, and the cooling stopping temperature is lower than the temperature, so that a martensitic structure is formed, and although the strength is improved, the toughness and the plasticity of the material are seriously reduced; too high a quench temperature, such as 600 c, will produce a pearlitic structure in the matrix, which is detrimental to plasticity. And (3) controlling the steel grade to be coiled within the range of 540-600 ℃ by combining the control difficulty of production, and then cooling to room temperature. When the coiling control temperature is lower than 540 ℃, the local temperature of the strip steel is easy to be too low, a martensite structure is easy to form, and the structure and the performance of the strip steel are not uniform.
In order to inhibit abnormal growth of ferrite grains in the strip steel after finish rolling and ensure that the strip steel structure is uniform equiaxial ferrite and a small amount of bainite structure, a front cooling mode is adopted for controlled cooling after rolling. Namely, the strip steel is quickly cooled by a first group of cooling water after being taken out of the hot continuous rolling unit, and the coiling at 540-600 ℃ can be realized.
The invention has the following advantages:
1. the steel has excellent comprehensive mechanical properties, the tensile strength is 280-380MPa, the elongation rate exceeds 40%, and meanwhile, the steel grade has excellent steel-aluminum interface bonding performance and is suitable for producing aluminum-coated strip steel. The aluminum-coated strip steel is insulated at 550 ℃ for 5h, and no iron-aluminum compound layer is formed on the steel-aluminum interface.
2. The steel has excellent plastic deformation capacity, meets the requirement of single-pass deformation of more than 80 percent, even more than 90 percent, does not need annealing in the middle, reduces the production procedures and improves the production efficiency.
3. The aluminum-clad steel strip has the advantages of uniform steel deformation, excellent stamping performance, good surface quality of an aluminum-clad finished product, no macroscopic stripe defect on the surface of the aluminum-clad steel strip, low cost and better steel-aluminum interface bonding performance, and can be used for replacing aluminum-clad plate strips.
4. The steel is produced by adopting a controlled rolling process, has simple production process and lower cost, and is suitable for large-scale production of enterprises.
Drawings
FIG. 1 is a schematic diagram of the static CCT curve (calculation) of the steel grade of the present invention.
FIG. 2 is a photograph showing a typical matrix structure of a steel according to an example of the present invention.
Detailed Description
The invention is further illustrated by the following examples and figures.
Example 1
According to the requirements of chemical components of steel, the steel is made in a 500kg vacuum induction furnace, the obtained chemical components are shown in table 1, 100kg steel ingots are cast, the heating temperature of steel billets is above 1180 ℃, the finishing temperature is 820-860 ℃, and the coiling temperature is 540-600 ℃.
The mechanical properties of the inventive steel examples are shown in table 2. The composition, production process and performance are compared with similar steel grades. Wherein,
the comparative steel 1 is Chinese patent CN101514426A 'low yield point steel for earthquake resistance of buildings with 100MPa yield strength and production method thereof'; the contents of Si and Al are high, and O is not contained;
the comparative steel 2 is Chinese patent CN101775535A '160 MPa-level earthquake-proof low yield point steel, steel plate and manufacturing method thereof', has higher Al content and does not contain O;
the comparative steel 3 is a novel special substrate for preparing an aluminum-coated steel strip, which is a Chinese patent CN101525720, and has over-high alloy components;
comparative steel 4 is a steel sheet for earthquake-resistant equipment and a production method thereof of Japanese patent JP09067652A, and has a high Al content.
The steel of the invention has obvious difference in composition with four kinds of comparative steel. The four types of comparative steel have higher Si and Al contents, while the steel grade of the invention clearly requires that the Al content is below 0.005 percent and Si is 0.005-0.15 percent; the requirement of the O content of the steel grade of the invention is obviously different from that of the comparative steel, the comparative steel has the control requirement on the O content, and the steel grade of the invention clearly requires to control the O content to be between 0.01 and 0.08 percent. Further, comparative steel 3 is required to have a high Mn content and extremely high upper limit of control of other alloy components, and comparative steel 2 is also required to contain a certain amount of Nb and V. So the composition of the comparative steel grade is obviously different from that of the steel grade of the invention.
From the performance, the comparative steels 1, 2 and 4 only need to have lower yield strength and higher elongation, but the steel grade of the invention clearly needs to have good steel-aluminum interface bonding performance besides the above requirements, is suitable for the production of aluminum-coated strip steel, and needs to have excellent stamping performance and good surface quality after aluminum coating; and simultaneously, the steel grade is required to have large cold rolling deformation capacity, so that the single-pass deformation is more than 80 percent, even more than 90 percent, and annealing is not needed in the middle, which is not possessed by the comparative steel 3. Therefore, the steel grade of the present invention is also significantly different from the comparative steel in properties.
In conclusion, the steel of the invention adopts the extremely low C-Si-Mn design, is supplemented with proper components such as P, S, Al, Ti, O and the like, designs the aluminum-coated substrate with the tensile strength of 280-plus 380, meets the requirements of the aluminum-coated substrate with high elongation, good steel-aluminum combination property, high surface quality and strong deformability, has short production period and simple process, and also meets or exceeds the requirements of the comparative steel types in performance.
Example 2
According to the composition requirements of the invention, the steel of the invention is smelted on a 500kg vacuum induction furnace in a laboratory. The chemical composition is shown in table 1. The heating temperature of the steel billet is 1200 ℃, the finish rolling temperature is 820-. The rolling thickness is 2-8 mm. The mechanical properties are shown in Table 2.
Table 1 inventive steel examples-chemical composition units: weight percent of
Figure BDA0001280947580000081
Table 2 steel examples of the invention-mechanical and aluminium clad properties
Figure BDA0001280947580000082
As can be seen from Table 2, the steel of the present invention has stable yield strength, tensile strength of various specifications of steel plates under different rolling processes is between 280-380MPa, and has high elongation. Is superior to the comparative steel grade in component design, production process and performance. Therefore, the steel can be widely used for producing double-sided large-deformation aluminum-clad strip steel, and the produced aluminum-clad strip has good stamping performance and surface quality.

Claims (5)

1. The steel for the high-surface-quality aluminum-coated substrate, which is suitable for large deformation and stamping processing, comprises the following chemical components in percentage by weight: c is less than or equal to 0.01 percent, Si: 0.006-0.015%, Mn: 0.05-0.3%, P is less than or equal to 0.015%, S is less than or equal to 0.01%, Al is less than or equal to 0.005%, N is less than or equal to 0.005%, Ti: 0-0.05%, O: 0.01-0.08%, and the balance of Fe and inevitable impurities; and, simultaneously:
C+N≤0.012；
Mn/S≥8；
Ti/(3.42N+4C)≥1；
the microstructure of the steel is uniform equiaxial ferrite and a small amount of bainite structure; the tensile strength of the steel is 280-380MPa, and the elongation is more than 40%.
2. The method for producing a steel for an aluminum-clad base plate with high surface quality which is adaptable to large deformation and press working according to claim 1, comprising,
1) smelting
The components according to claim 1 are pretreated by molten iron, blown at the top and the bottom of a converter, refined outside the furnace and cast into a plate blank continuously;
2) reheating the plate blank, wherein the heating temperature is 1180-1220 ℃;
3) controlled rolling
Two-stage controlled rolling is adopted, the finish temperature of rough rolling is over 980 ℃, and the accumulated deformation in the rough rolling stage is more than or equal to 80 percent; the inlet temperature of finish rolling is above 950 ℃, and the finish rolling finishing temperature is 820-860 ℃;
4) controlling cooling at a water cooling speed of more than 10 ℃/s;
5) and (4) coiling at the coiling temperature of 540-600 ℃.
3. The method of producing a steel for an aluminum-clad base plate with high surface quality which is suitable for large deformation and press working according to claim 2, wherein the side pressure in the rough rolling stage is controlled to be within 50mm in the step 3).
4. The method for producing a steel for an aluminum-clad base plate with high surface quality which is suitable for large deformation and press working according to claim 2, wherein the microstructure of the steel is a uniform equiaxed ferrite structure plus a small amount of bainite structure.
5. The method for producing a steel for a high-surface-quality aluminum-clad substrate, which is suitable for large deformation and press working, according to claim 2, 3 or 4, wherein the steel has a tensile strength of 280 to 380MPa and an elongation of 40% or more.
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