CN111349851B - Steel for aluminum-coated substrate and manufacturing method thereof - Google Patents

Steel for aluminum-coated substrate and manufacturing method thereof Download PDF

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CN111349851B
CN111349851B CN201811580471.9A CN201811580471A CN111349851B CN 111349851 B CN111349851 B CN 111349851B CN 201811580471 A CN201811580471 A CN 201811580471A CN 111349851 B CN111349851 B CN 111349851B
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steel
aluminum
less
equal
clad substrate
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CN111349851A (en
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宋凤明
王巍
胡晓萍
张华伟
杨阿娜
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/02Ferrous alloys, e.g. steel alloys containing silicon
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING 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
    • C21D8/00Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING 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
    • C21D8/00Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226Hot rolling
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/001Ferrous alloys, e.g. steel alloys containing N
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/002Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/004Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/04Ferrous alloys, e.g. steel alloys containing manganese
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/14Ferrous alloys, e.g. steel alloys containing titanium or zirconium

Abstract

The invention discloses steel for an aluminum-coated substrate, which comprises the following chemical elements in percentage by mass: c is more than 0 and less than or equal to 0.01 percent, Si is more than 0 and less than or equal to 0.005 percent, Mn: 0.08-0.2%, P: 0.018-0.03%, Al is less than or equal to 0.005%, N: 0.0040 to 0.010% and Ti: 0.01-0.035%, O: 0.02-0.050%, and the balance of Fe and other inevitable impurities. In addition, the invention also discloses a manufacturing method of the steel for the aluminum-coated substrate, which comprises the following steps: (1) smelting and casting; 2) reheating: the casting blank is reheated to 1180-1250 ℃; (3) rough rolling; (4) fine rolling; (5) coiling; (6) and cooling to room temperature. The steel for the aluminum-clad substrate has good mechanical property, high strength and good plasticity.

Description

Steel for aluminum-coated substrate and manufacturing method thereof
Technical Field
The present invention relates to steel and a method for manufacturing the same, and more particularly, to steel for a substrate and a method for manufacturing the same.
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 strip steel by rolling at room temperature to form a surface of aluminum and a core layer of steel, has the strength of the existing steel, has the characteristics of good heat dissipation, corrosion resistance, light weight and attractive appearance of the aluminum, particularly greatly reduces the cost, and is widely applied to the fields of household electrical panels, heat dissipation parts, decoration and the like.
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 that of aluminum, and therefore, the substrate is generally low in strength and excellent in plasticity. However, the aluminum-clad substrate also requires good steel-aluminum lamination performance, and the low yield strength steel in the general sense is difficult to be used for aluminum-clad steel production.
Chinese patent publication No. CN102019727A, published as 2011, 4/20/entitled "aluminum-coated steel strip for cooler, method for producing same, and steel strip and aluminum alloy strip used for same" discloses an aluminum-coated steel strip, method for producing same, and steel strip and aluminum alloy strip used for same. The technical proposal disclosed in the Chinese patent document relates to the used substrate, but the technical proposal is mainly used for producing thicker aluminum-coated strip steel, has insufficient plastic deformation capability and is difficult to meet the requirement of large deformation.
Chinese patent publication No. CN101525720, published as 2009, 9.9.9, entitled "a novel special base steel strip for producing an aluminum-coated steel strip" discloses a novel special base steel strip for producing an aluminum-coated steel strip. In the technical scheme disclosed in the Chinese patent document, the related steel is a high alloy component, wherein the content of Mn is 15-30%.
Chinese patent publication No. CN107881427A, published as 2018, 4, 6 and entitled "a low yield strength aluminum-clad substrate with excellent plasticity" discloses a low yield strength aluminum-clad substrate, which requires that the content of P is controlled to 0.01% in order to ensure the steel-aluminum bonding performance and other mechanical performance indexes, which obviously increases the production difficulty of steel plates.
Therefore, the steel related in the prior art does not have steel-aluminum bonding performance on one hand, and only has strength plasticity equivalent to that of Al; on the other hand, in the prior art relating to the aluminum-clad substrate, the P content is generally limited, and the production difficulty of the aluminum-clad substrate is greatly increased.
Disclosure of Invention
The invention aims to provide the steel for the aluminum-clad substrate, which adopts an extremely low C-Si component system, relaxes the content limit of P, and obtains proper strength and good plasticity on the basis of ensuring the bonding performance of steel and aluminum.
In order to achieve the purpose, the invention provides steel for an aluminum-coated substrate, which comprises the following chemical elements in percentage by mass:
c is more than 0 and less than or equal to 0.01 percent, Si is more than 0 and less than or equal to 0.005 percent, Mn: 0.08-0.2%, P: 0.018-0.03%, Al is less than or equal to 0.005%, N: 0.0040 to 0.010% and Ti: 0.01-0.035%, O: 0.02-0.050%, and the balance of Fe and other inevitable impurities.
In the steel for the aluminum-clad substrate, the low C-Si-Mn design with the components similar to pure iron is adopted, and a proper amount of P and Ti are added, because the control of the steel components of the steel for the aluminum-clad substrate is extremely strict, particularly the addition amount of certain alloy components is limited for ensuring good steel-aluminum interface bonding performance, and meanwhile, the conventional alloy components have definite control requirements, which are obviously different from common steel types, the inventor designs the mass percent ratio of the chemical elements through a large amount of experimental research and analysis, and the design principle of each chemical element is as follows:
c: in the steel for an aluminum-clad substrate according to the present invention, C increases the yield strength of the steel sheet by solid solution strengthening, and decreases the elongation. The content of C should be reduced as much as possible according to the actual steel making process, so the mass percent of C in the steel for the aluminum-clad substrate is controlled to be 0 < C < 0.01, wherein, the mass percent of C is preferably 0.002-0.006%.
Si: in the technical scheme of the invention, Si is a deoxidizing element and is also a solid solution strengthening element, and for the technical scheme of the invention, the yield strength of the steel plate can be increased and the elongation can be reduced by adding Si, and Si exceeding the upper limit of the content of the scheme can deteriorate the composite performance of a steel-aluminum interface, so that the mass percent of Si in the steel for the aluminum-clad substrate is controlled to be more than 0 and less than or equal to 0.005 percent.
Mn: mn is an essential element for steelmaking deoxidation, and can simultaneously expand an austenite region, reduce the transformation temperature of super-cooled austenite, promote the transformation of medium and low temperature structures and refine the microstructure of steel, so that Mn is an important strengthening and toughening element. In addition, for the solution of the present invention, the addition of Mn increases the strength and also decreases the plasticity, and the higher content of Mn also increases the manufacturing cost. Therefore, the mass percent of Mn in the steel for the aluminum-clad substrate is controlled to be 0.08-0.2%.
P: p is likely to segregate at grain boundaries, and the bonding energy of the grain boundaries is reduced, so that the steel sheet becomes brittle. The P is added into the free-cutting steel, so that the chips can be prevented from sticking on the cutter, and the service life of the cutter is prolonged. In the steel system of the technical scheme, the fifth group element in the periodic table of the elements of P and N is found to have the property similar to that of N, and the steel of the technical scheme can inhibit the diffusion of Al, so that the steel particularly plays a role in making a brittle steel-aluminum compound layer difficult to form on a steel-aluminum interface, thereby obviously improving the steel-aluminum bonding performance and playing an important role in realizing the technical effect of the scheme. On the other hand, however, in the present invention, P exceeding the upper limit of the content is disadvantageous to the toughness and elongation of the steel grade of the present invention, and therefore, the mass percentage of P in the steel for an aluminum-clad substrate of the present invention is controlled to 0.018 to 0.03%, and preferably, the mass percentage of P may be further controlled to 0.018 to 0.024%.
Al: in the steel for an aluminum-clad substrate according to the present invention, Al is an element necessary for deoxidation and also increases the strength of the steel, but Al having a high content is easily diffused to the steel-aluminum bonding interface to deteriorate the interface bonding strength. Therefore, in the technical scheme of the invention, the mass percent of Al is required to be controlled so as to avoid influencing the combination property of steel and aluminum, and the mass percent of Al in the steel for the aluminum-clad substrate is controlled to be less than or equal to 0.005 percent.
N: in the steel for the aluminum-clad substrate according to the present invention, N can form AlN particles with Al in the steel, thereby suppressing diffusion of Al to the interface, but a high N solid solution content can significantly improve the strength of the steel and is disadvantageous in plasticity. Therefore, in the steel for an aluminum-clad substrate according to the present invention, the mass percentage of N is controlled to 0.0040 to 0.01%, and preferably, the mass percentage of N may be further controlled to 0.004 to 0.008%.
Ti: in the steel for an aluminum-clad substrate according to the present invention, Ti was used to fix C, N atoms to reduce its effect of inhibiting dislocation movement. Ti is a strong ferrite-forming element and a carbonitride-forming element. In the Ti-added steel, a proper amount of nitrogen and titanium form titanium nitride, the formation temperature is above 1400 ℃, and the titanium nitride is precipitated in a high-temperature liquid phase or delta ferrite. Wherein Ti4C2S2The precipitation is started at 1260 ℃, TiC is precipitated at 1050 ℃, and fine precipitates can be nailed to grain boundaries, so that austenite grains are refined, the grains in a welding heat affected zone are prevented from growing, and the welding performance of the steel plate is improved. Ti can preferentially bind N in the steel and reduce the amount of AlN in the steel. However, more Ti coarsens TiC and TiN particles, so that the grain boundary pinning effect is lost, the elongation of the steel plate is reduced, and the manufacturing cost is increased. Therefore, in the steel for an aluminum-clad substrate according to the present invention, the mass percentage of Ti is limited to 0.01 to 0.035%. In some preferred embodiments, it is further defined that N, Ti satisfies the relationship 2.5 Ti/N5.0 by mass percent.
O: in the steel for an aluminum-clad substrate according to the present invention, the contents of Si and Al are limited to extremely low ranges in the aspect of the present invention, and therefore, the oxygen content in the steel is inevitably high. However, the oxygen element can suppress adverse effects of the Al element in the steel on the interface bonding of steel and aluminum, but at the same time, considering that an excessively high content of oxygen tends to form non-metallic inclusions, which are detrimental to the fatigue properties and toughness of the steel sheet, the mass percentage of O is limited to 0.02 to 0.050% and preferably 0.02 to 0.04% in the steel for an aluminum-clad substrate according to the present invention. In some preferred embodiments, O, Al and Si may be further defined to satisfy O/(0.9Al +1.2Si) ≧ 3.0.
In conclusion, according to the technical scheme, through the collocation of the chemical element components, especially through the addition of P as a beneficial element, the production difficulty is reduced, the production process is simplified, the production efficiency is improved, and the steel for the aluminum-coated substrate with excellent performance is obtained.
Further, the steel for an aluminum-clad substrate according to the present invention further satisfies: 2.5 or more Ti/N or less than 5.0, and O/(0.9Al +1.2Si) or more than 3.0.
In the above formulas, Ti, N, O, Al, and Si each represent a mass percentage thereof, and the numerical value assigned to the above formula is a numerical value before the percentile, for example, when the mass percentage of Ti is 0.021% and the mass percentage of N is 0.0065%, the formula Ti/N is 0.021/0.0065 is 3.23.
Further, in the steel for the aluminum-clad substrate, the mass percentage of each chemical element also satisfies at least one of the following:
C:0.002-0.006%,P:0.018-0.024%,N:0.004-0.008%,O:0.02-0.04%。
further, in the steel for an aluminum-clad substrate according to the present invention, among other inevitable impurities: s is less than or equal to 0.005 percent.
Further, in the steel for an aluminum-clad substrate according to the present invention, the matrix is equiaxed ferrite, and the ferrite grain size is 10 to 50 μm.
Furthermore, in the steel for the aluminum-coated substrate, the yield strength is 160-240MPa, the tensile strength is more than or equal to 280MPa, and the elongation is more than or equal to 40%.
Accordingly, another object of the present invention is to provide a method for manufacturing the above steel for aluminum-clad base plate, which uses high temperature hot rolling, and has the advantages of simple production process, low production cost, low yield strength of the obtained steel for aluminum-clad base plate, and good plasticity and steel-aluminum combination property.
In order to achieve the above object, the present invention provides a method for manufacturing the steel for an aluminum-clad substrate, comprising the steps of:
(1) smelting and casting;
(2) reheating: the casting blank is reheated to 1180-1250 ℃;
(3) rough rolling;
(4) fine rolling;
(5) coiling;
(6) and cooling to room temperature.
In the manufacturing method, the solid solution effect of the alloy elements in the casting blank is comprehensively considered, so that the casting blank is controlled to be reheated at 1180-1250 ℃. Followed by rough rolling, finish rolling, coiling and cooling to obtain the desired steel sheet. Because the steel for the aluminum-coated substrate is ultra-low carbon steel and the addition amount of alloy elements is small, the substrate of the steel is a typical equiaxial ferrite structure, and the grain size of the ferrite is 10-50 microns.
Further, in the manufacturing method of the present invention, in the step (3), the accumulated deformation amount in the rough rolling stage is not less than 80%, and the finish temperature of the rough rolling is 950 ℃ to 1150 ℃.
Further, in the manufacturing method of the present invention, in the step (4), the finish rolling temperature of the finish rolling is controlled to 840-920 ℃.
Further, in the manufacturing method of the present invention, in the step (5), the finish-rolled steel sheet is water-cooled to 580-640 ℃ and coiled.
Compared with the prior art, the steel for the aluminum-clad substrate and the manufacturing method thereof have the following advantages and beneficial effects:
the steel for the aluminum-coated substrate has excellent comprehensive mechanical properties, the yield strength is 160-240MPa, the tensile strength is more than or equal to 280MPa, and the elongation rate exceeds 40%.
In addition, the steel for the aluminum-clad substrate has excellent steel-aluminum interface bonding performance, and the thickness of a steel-aluminum interface compound layer of the steel for the aluminum-clad substrate after final high-temperature brazing is less than or equal to 5 microns, and can even be completely eliminated in some preferred embodiments, so that the steel-aluminum interface of the steel for the aluminum-clad substrate is clean and is very suitable for producing aluminum-clad strip steel.
Moreover, the steel for the aluminum-clad substrate widens the mass percentage range of P to 0.018-0.03%, reduces the production difficulty, simplifies the production process and improves the production efficiency.
In addition, the steel for the aluminum-clad substrate has excellent plastic deformation capacity, can meet the requirement of single-pass large deformation in the aluminum-clad rolling process, does not need annealing in the middle, reduces the production procedures and improves the production efficiency.
Besides the advantages and beneficial effects, the manufacturing method provided by the invention has the advantages that the manufacturing method is simple in production process and low in cost, and is very suitable for large-scale production of enterprises due to the fact that high-temperature hot rolling is adopted.
Drawings
Fig. 1 shows the microstructure of the steel for an aluminum-clad substrate of example 1.
Detailed Description
The steel for an aluminum-clad substrate and the method for manufacturing the same according to the present invention will be further explained and explained with reference to the following specific examples and drawings attached to the specification, but the explanation and explanation do not unduly limit the technical solution of the present invention.
Examples 1 to 8
Table 1 shows the mass percentages (wt%) of the respective chemical elements in the steels for aluminum-clad substrates of examples 1 to 8.
TABLE 1 (wt%, balance Fe and unavoidable impurity elements other than S)
As can be seen from Table 1, in comparison with the prior art, the mass percentages of Si and Al in the examples are below 0.005%, the mass percentage of O is between 0.02 and 0.05%, and the mass percentage of N is between 0.0040 and 0.010%. In addition, P is added as a favorable element, so that the mass percent of P is controlled to be 0.018-0.03%.
The manufacturing method of the steel for the aluminum-clad substrate of examples 1 to 8 was manufactured by the following steps:
(1) smelting and casting: according to the chemical element components shown in Table 1, the casting blank is obtained by smelting on a 500kg vacuum induction furnace and casting.
(2) Reheating: the cast slab is reheated to 1180 ℃ -1250 ℃.
(3) Rough rolling: the accumulated deformation in the rough rolling stage is more than or equal to 80 percent, and the rough rolling finishing temperature is 950-1150 ℃.
(4) Finish rolling: the finish rolling temperature of the finish rolling is controlled to be 840-920 ℃.
(5) Coiling: and (3) cooling the steel plate after the finish rolling to 580-640 ℃ by water, and coiling.
(6) And cooling to room temperature.
In step (5), the cooling method for coiling may be air cooling other than water cooling, for example, when the steel for aluminum-clad substrate is thin, such as less than or equal to 3.0mm, the steel for aluminum-clad substrate may be cooled to a desired coiling temperature before entering the coiler, and the performance may be satisfied.
Table 2 lists the specific process parameters involved in the method of making the steel for aluminum-clad substrates of examples 1-8.
Table 2.
The tests were carried out on the steels for aluminum-clad substrates of examples 1 to 8, and the test results are shown in Table 3.
Table 3.
As can be seen from Table 3, the steel for the aluminum-clad substrate in each example of the present application has stable yield strength, and the yield strength of the steel plates of various specifications is between 160 and 240MPa, the tensile strength is not less than 280MPa, and the elongation is very high (the elongation is not less than 40%).
In addition, as can be seen from table 3, the steel for aluminum-clad substrates of the examples of the present invention has excellent steel-aluminum interface bonding performance, and the thickness of the steel-aluminum interface compound layer of the steel for aluminum-clad substrates after aluminum cladding is less than or equal to 5 μm, while in some other preferred embodiments, the thickness of the steel-aluminum interface compound layer can even be completely absent.
Fig. 1 shows the microstructure of the steel for an aluminum-clad substrate of example 1. As shown in fig. 1, the matrix of the steel for an aluminum-clad substrate of example 1 was equiaxed ferrite, and the ferrite grain size was 10 to 50 μm.
As can be seen from tables 1 to 3 and fig. 1, the steel for the aluminum-clad substrate in each embodiment of the present invention adopts an extremely low C — Si — Mn design, supplemented with a small amount of Ti, N, O and a proper amount of P, and the obtained steel for the aluminum-clad substrate satisfies the requirements of the aluminum-clad substrate of high elongation, good steel-aluminum combination property and strong deformability.
Compared with the prior art, the steel for the aluminum-clad substrate and the manufacturing method thereof have the following advantages and beneficial effects:
the steel for the aluminum-coated substrate has excellent comprehensive mechanical properties, the yield strength is 160-240MPa, the tensile strength is more than or equal to 280MPa, and the elongation rate exceeds 40%.
In addition, the steel for the aluminum-clad substrate has excellent steel-aluminum interface bonding performance, and the thickness of a steel-aluminum interface compound layer of the steel for the aluminum-clad substrate after final high-temperature brazing is less than or equal to 5 microns, and can even be completely eliminated in some preferred embodiments, so that the steel-aluminum interface of the steel for the aluminum-clad substrate is clean and is very suitable for producing aluminum-clad strip steel.
Moreover, the steel for the aluminum-clad substrate widens the mass percentage range of P to 0.018-0.03%, reduces the production difficulty, simplifies the production process and improves the production efficiency.
In addition, the steel for the aluminum-clad substrate has excellent plastic deformation capacity, can meet the requirement of single-pass large deformation in the aluminum-clad rolling process, does not need annealing in the middle, reduces the production procedures and improves the production efficiency.
Besides the advantages and beneficial effects, the manufacturing method provided by the invention has the advantages that the manufacturing method is simple in production process and low in cost, and is very suitable for large-scale production of enterprises due to the fact that high-temperature hot rolling is adopted.
It should be noted that the prior art in the protection scope of the present invention is not limited to the examples given in the present application, and all the prior art which is not inconsistent with the technical scheme of the present invention, including but not limited to the prior patent documents, the prior publications and the like, can be included in the protection scope of the present invention.
In addition, the combination of the features in the present application is not limited to the combination described in the claims of the present application or the combination described in the embodiments, and all the features described in the present application may be freely combined or combined in any manner unless contradictory to each other.
It should also be noted that the above-mentioned embodiments are only specific embodiments of the present invention. It is apparent that the present invention is not limited to the above embodiments and similar changes or modifications can be easily made by those skilled in the art from the disclosure of the present invention and shall fall within the scope of the present invention.

Claims (8)

1. The steel for the aluminum-coated substrate is characterized by comprising the following chemical elements in percentage by mass:
c is more than 0 and less than or equal to 0.01 percent, Si is more than 0 and less than or equal to 0.005 percent, Mn: 0.08-0.2%, P: 0.021-0.03%, Al is less than or equal to 0.005%, N: 0.0040 to 0.010% and Ti: 0.01-0.035%, O: 0.02-0.050%, and the balance of Fe and other inevitable impurities;
the matrix of the steel for the aluminum-coated substrate is equiaxed ferrite, and the grain size of the ferrite is 10-50 microns; the thickness of the steel-aluminum interface compound layer of the steel for the aluminum-coated substrate after the final high-temperature brazing is less than or equal to 5 mu m;
the chemical elements also meet the following mass percentage: 2.5 or more Ti/N or less than 5.0, and O/(0.9Al +1.2Si) or more than 3.0.
2. The steel for the aluminum-clad substrate as claimed in claim 1, wherein the chemical elements further satisfy at least one of the following contents by mass:
C:0.002-0.006%,P:0.021-0.024%,N:0.004-0.008%,O:0.02-0.04%。
3. the steel for an aluminum-clad substrate as recited in claim 1, wherein, among other inevitable impurities: s is less than or equal to 0.005 percent.
4. The steel for an aluminum-clad substrate as claimed in any one of claims 1 to 3, wherein the yield strength is 160-240MPa, the tensile strength is 280MPa or more, and the elongation is 40% or more.
5. The method for producing a steel for an aluminum-clad substrate as recited in any one of claims 1 to 4, comprising the steps of:
(1) smelting and casting;
(2) reheating: the casting blank is reheated to 1180-1250 ℃;
(3) rough rolling;
(4) fine rolling;
(5) coiling;
(6) and cooling to room temperature.
6. The manufacturing method according to claim 5, wherein in the step (3), the accumulated deformation amount in the rough rolling stage is not less than 80%, and the finish temperature of the rough rolling is in the range of 950 ℃ to 1150 ℃.
7. The manufacturing method according to claim 5, wherein in the step (4), the finish rolling temperature of the finish rolling is controlled to 840-920 ℃.
8. The manufacturing method according to claim 5, wherein in the step (5), the finish-rolled steel sheet is water-cooled to 580-640 ℃ and coiled.
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