SE1551047A1 - Superstrength cold rolled weathering steel sheet and methodof manufacturing the same - Google Patents

Superstrength cold rolled weathering steel sheet and methodof manufacturing the same Download PDF

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SE1551047A1
SE1551047A1 SE1551047A SE1551047A SE1551047A1 SE 1551047 A1 SE1551047 A1 SE 1551047A1 SE 1551047 A SE1551047 A SE 1551047A SE 1551047 A SE1551047 A SE 1551047A SE 1551047 A1 SE1551047 A1 SE 1551047A1
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steel sheet
superstrength
cold
sheet according
manufacturing
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SE1551047A
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SE539940C2 (sv
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Yong Zhong
Li Wang
Weijun Feng
Xiaoming He
Junjie Huang
Yanglin Ke
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Baoshan Iron & Steel
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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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • C21D1/613—Gases; Liquefied or solidified normally gaseous material
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    • C21D6/00—Heat treatment of ferrous alloys
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
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    • 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
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    • 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
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • 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
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    • 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
    • C21D8/0236—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
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
    • C21D8/1233—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
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1272—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with 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
    • C21D2211/008—Martensite
    • 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
    • C21D8/0273—Final recrystallisation annealing

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Description

15 20 25 30 wherein, the ranges (wt%) of chemical compositions of the molten steel are: C: less than or equal to 0.08%; Si:0.25~ 0.75%; Mn:0.8~2.0%; P: 0.070~0.150%; S: less than or equal to 0.040%; Cu: 0.25~0.60 %; Cr: 0.30~1.25wt%; Ni: less than or equal to 0.65%; V: 0.05~0.20%; N: 0.015~0.030%.
[0004] US patent of Publication No.US6056833, published on May 2, 2000 and titled “thermomechanically controlled processed high strength weathering steel with low yield/tensile ratio” relates to a weathering steel sheet with a low yield/tensile ratio that has a minimum yield strength of 70-75 ksi and a yield/tensile ratio less than or equal to about 0.85. The chemical compositions of the weathering steel sheet consists (wt%) of C: 0.08~0.12%; Mn: 0.80~1.35%; Si: 0.30~0.65%; Mo: 0.08~0.35%; V: 0.06~0.14%; Cu: 0.20~0.40%; Ni: 0.50%; Cr: 0.30~0.70%; P: 0.010~0.020%; Nb: less than or equal to 0.04%; Ti: less than or equal to 002%; S: less than or equal to 0.01%; the remainders thereof being Fe and other unavoidable impurities.
[0005] Korean patent of Publication No.KR431839, published on May 20, 2004, and titled “method of producing cold rolled weathering steel sheet”, discloses a method of producing the cold rolled atmosphere corrosion resistant steel sheet, wherein , the chemical compositions of the steel sheet consist of C: 0.06~0.08 vvt%; Si: 0.17~0.24 vvt%; Mn: 0.9~1.10 vvt%; P: less than or equal to 0.020 vvt%; S: less than or equal to 0.010 vvt%; Cu: 0.20~0.30vvt%; Ni: 0.20~0.30 vvt%; H: less than or equal to 2.5 ppm, the remainders thereof being Fe and other unavoidable impurities. The steel sheet has a tensile strength of more than or equal to 45 kgf/mmz, a yield strength of more than or equal to 32kgf/mm2, and an elongation rate of more than or equal to 22%.
[0006] to produce the weathering steel sheet, and due to the limitation with respect to the The aforementioned first and second patents use hot rolling processes thickness of steel sheet in hot rolling units, the weathering steel sheet produced in hot rolling process has often a large thickness, and further, the limit thickness of available the hot rolling steel sheet increases with the improvement of the strength thereof. Besides, the shape and surface quality of the hot rolling steel sheet is still poor than that of cold rolling steel sheet. Although the above third patent adopts 20 25 cold rolling process to produce the weathering steel, the steel sheet presents a low strength(the yield strength is only 300MPa) , which cannot be widely used in the production of high strength steel structures.
SUMMARY
[0007] superstrength cold rolled weathering steel sheet, that has a large strength, a small thickness, excellent resistance to atmosphere corrosion resistant, good shape and One of the objectives of the present invention is to provide a surface quality, so as to accommodate with the tendency of thinner and lighter steel structures; additionally, it does not contain the element Si, thereby improving the manufacturability of the materials, nor the element Nb, thereby reducing the production cost.
[0008] proposes a superstrength cold rolled weathering steel sheet, the weight To achieve the aforementioned objectives, the present invention percentage of the chemical elements of which are as follows: C: 0.05~0.16%; Mn: 1.00~2.20%; Al: 0.02~0.06%; Cu: O.20~0.40%; Cr: O.40~0.60%; Ti: 0.015~0.035%; P: less than or equal to 0.03%; the remainders thereof being Fe and other unavoidable impurities. The unavoidable impurities in this technical solution consist primarily of elements S and N; and further includes unavoidable residual trace element Si.
[0009] Preferably, the weight percentage of the chemical elements of the superstrength cold rolled weathering steel sheet are further defined as follows: C: 0.07~0.15°/0; Mn: 1.30~2.00%; Al: 0.02~0.04%; 10 15 20 25 Cu: O.25~0.35%; P: less than or equal to O.15%.
[0010] more beneficial in practice.
The preferable composition ratio above can make the technical solution
[0011] steel sheet further includes Ni of less than 0.20wt%, and a suitable amount of Ni Preferably, the above-mentioned superstrength cold rolled weathering is added to further improve the weathering performance of the steel sheet.
[0012] cold rolled weathering steel sheet is martensite, the volume fraction of which is Furthermore, the microstructure of the above-mentioned superstrength more than 95%.
[0013] rolled weathering steel sheet is 0.8~1.5mm.
Furthermore, the thickness of the above-mentioned superstrength cold
[0014] rolled weathering steel sheet as mentioned in this invention is as follows: The design principle of the chemical elements of the superstrength cold
[0015] improve the hardenability and strength effectively. The present invention relates to C: C is the most fundamental strengthening element in steel, able to a weathering steel subjected to high hydrogen cooling, which has a maximum cooling speed of 150°C/s. The content of C has to be more than 0.05% in order to achieve martensite phase transformation. But if it is more than 0.16%, the welding performance of the steel may not meet the demand in use. ln light of this and taking the strength and operational performance of the material into account, the content of C in the present invention is controlled in the range of 0.05~0.16vvt%.
Preferably, the range thereof is 0.07~0.15wt%.
[0016] the strength of the steel sheet. To obtain the steel in the present invention that Mn: Mn is a solid solution strengthening element, benefitting for improve has a yield strength of more than or equal to 7OOMPa, and a tensile strength of more than or equal to 1000MPa, the content of Mn has to be more than 1.0%. But excessive Mn may result in the reduction of the welding performance and 10 15 20 25 30 inadequacy of the elongation rate. To meet the demand that the elongation rate is more than or equal to 5%, the content of Mn should be less than equal to 2.2%. ln sum, the content of Mn in the present invention is designed to be 1.00~2.20wt%, and further, 1.30~2.00wt%. Both C and Mn have the effect of improving the strength of the material and reducing the welding performance thereof, hence, the content of them cannot be the maximum or minimum value in the present invention. ln order to meet the above requirements, the relationship between the compositions C and Mn is designed to be: 0.19% invenüon.
[0017] invention is required to be of good cold bending property, but excessive content of Al: the addition of Al aims for deoxidization. The steel in the present O may result in the degradation of the formation performances of the material, like cold bending. ln order to satisfy the demand on the formation performances of the steel, the content of Al should not be less than 0.02%. However, excessive Al may result in too many impurities such as AlN in the steel sheet, reducing the elongation rate of the material. ln light of this, taking both the deoxidization impurities into account, the content of carbon should be controlled in 0.02~0.06%, and preferably, 0.02~0.04%.
[0018] and P between the base strip and the rust layer, which bonds tightly with the base Cu: Cu involves in forming a barrier with the primary components Cu strip to protect the same well. Furthermore, Cu can also compensate the impairment of impurity element S in the steel sheet. ln order to ensure the weathering performance required by the steel sheet in the present invention, the content of Cu should not be less than 0.2%. But the addition of excessive Cu may cause serious problem such as “Cu brittleness”. The maximum amount of Cu should be 0.4%, in such a way to coordinate with the addition of the element Ni.
Accordingly, in the present invention, the content of Cu in the superstrength cold rolled weathering steel sheet should be set in 0.20~0.40wt%, and in the preferred solution, the content may be set in O.25~O.35%.
[0019] steel sheet, so as to improve the ability of deactivation of the steel sheet, and Cr: Cr involves in forming an dense oxidized film on the surfaces of the 10 15 20 25 30 especially when Cr and Cu are added into steel simultaneously, the effect is more obvious; in the present technical solution, it is needed that the weight percentage of Cr should be controlled in O.40~0.60%. [oo2o1 improve the formation performance of the steel sheet through precipitation Ti: Ti is the main element for the formation of carbonitride, which can strengthening and fine crystal strengthening. Accordingly, the weight percentage of Ti in the present invention should be designed to be in 0.015~0.035%.
[0021] steels, P together with Cu in the present invention may form a barrier for resisting P: specifically speaking, although P is the impurity element in most erosion, thereby improving the performance of the atmosphere corrosion resistance of the steel sheet; at the same time, it has an effect of solid solution strengthening. However, excessive P may increase the brittleness of the steel and degrade the welding performance thereof, whereby the weight percentage of P should be controlled to be less than or equal to 0.030% and preferably less than or equal to 0.015%.
[0022] caused by the addition of Cu. ln order to obtain good effect and reduce the cost, the ratio of Cu and Ni should be less than or equal to 2/3. Based on this, the content of Ni in the present invention is designed to be less than or equal to 0.2%.
Ni: the addition of Ni aims for alleviating the problem of “Cu brittleness”
[0023] with the aforementioned superstrength cold rolled weathering steel sheet. This The present invention further provides a container panel manufactured container panel has a good shape and superior surface quality.
[0024] manufactured with the aforementioned superstrength cold rolled weathering steel The present invention further provides a vehicle structure panel sheet. This vehicle structure panel has a light weight and a high strength.
[0025] manufacturing the aforementioned superstrength cold rolled weathering steel Correspondingly, the present invention further provides a method of sheet, comprising the following stages: smelting, heating and preservation, hot rolling, coiling, pickling, cold rolling, continuous annealing, skin passing; wherein, in the continuous annealing process, the annealing temperature is 830~880°C so 10 15 20 25 as to enable the complete austenization, then the steel is cooled rapidly in an high hydrogen atmosphere so as to attain martensite structure.
[0026] continuous annealing process and the annealing temperature higher than that in ln the manufacturing process, the present invention adopts the the prior art, so as to ensure the austenization before the steel sheet is cooled rapidly. The temperature can be controlled by adjusting the extent of austenization, in order to modulate the mechanical and forming properties of the finished products. ln the process of rapid cooling, the high hydrogen atmosphere is utilized for rapid cooling, to obtain martensite micro-structure therein; comparing to the water quenching process, the cooling effect in rapid cooling process in the high hydrogen atmosphere is more even, thereby not only reducing the production cost of steel, but also obtaining more excellent shape and surface quality.
[0027] volume fraction of hydrogen in the high hydrogen atmosphere is 60%.
Furthermore, in the stage of continuous annealing process above, the
[0023] cooling speed of the rapid cooling is more than 100°C/s.
Furthermore, in the stage of continuous annealing process above, the
[0029] temperature is further defined as 850~880°C, in order to achieve better effect.
Preferably, in the continuous annealing process above, the annealing
[0030] is heated and preserved at 1170~1200°C. The technical solution adopts low Furthermore, in the stages of heating and preservation above, the slab heating and preserving temperatures, in order to reduce the adverse effect by Cu on the thermoplastic performance of the steel, under the premise of ensuring the complete soluting of the C, N compound.
[0031] temperature is more than or equal to Ar3.
Furthermore, in the stage of hot rolling above, the finish rolling
[0032] 450~550°C. The technical solution adopts a low coiling temperature which is Furthermore, in the stage of coiling above, the coiling temperature is good for alleviating the problem of squashing after the steel coil is uncoiled, while fine precipitated phase can be obtained in the steel sheet. 10 15 20 25
[0033] Furthermore, in the stage of cold rolling above, the reduction rate therein is 50~60%.
[0034] with the reasonable composition design and suitable technological processes, The superstrength cold rolled weathering steel sheet in the invention, presents superior effect in practice: it presents excellent performance of atmosphere corrosion resistance; high strength, i.e., the yield strength more than 700MPa and the tensile strength more than 1000MPa; good shape and surface quality.
DETAILED DESCRIPTION
[0035] detailed embodiments, to further specify the superstrength cold rolled weathering Hereinafter, a detailed description will be given in conjunction with the steel sheet and the method thereof in the present invention, which, however, do not constitute the improper limitation on the present technical solution.
[0036] Embodiments 1~7.
[0037] as the following stages: The superstrength cold rolled weathering steel sheet is manufactured
[0038] elements therein as shown in Table 1; (1) smelting and controlling the weight percentage of the chemical
[0039] (2) heating and preserving the slab at temperature of 1170~1200°C;
[0040] (3) hot rolling: the finish rolling temperature is more than or equal to Ar3;
[0041] (4) coiling: the coiling temperature is 450~550°C;
[0042] (5) pickling;
[0043] (6) cold rolling: the cold rolling reduction rate is 50~60%;
[0044] (7)continuous annealing: the annealing temperature is 830~880°C so as to enable the complete austenization, then the steel is cooled rapidly (the cooling 10 speed is more than 100°C/s) in high hydrogen atmosphere (the volume fraction of hydrogen therein is 60%.) so as to attain martensite structure;
[0045] (8) skin passing.
[0046] superstrength cold ro||ed weathering steel sheet in Embodiments 1~7.
Table 1 lists the weight percentage of the chemical elements in the
[0047] Table 1 (wt%, the remainders being Fe and other unavoidable impurities) No. C Mn Al Cu Cr Ni Ti P Embodiment1 0.08 1.8 0.04 0.35 0.45 - 0.030 0.01 Embodiment2 0.10 1.7 0.04 0.3 0.5 - 0.035 0.01 Embodiment3 0.14 1.4 0.03 0.25 0.5 - 0.02 0.01 Embodiment4 0.15 1.2 0.04 0.3 0.55 - 0.015 0.01 Embodiment5 0.06 2.2 0.06 0.4 0.4 0.1 0.03 0.01 Embodiment6 0.11 1.6 0.03 0.25 0.6 0.15 0.025 0.01 Embodiment7 0.16 1.0 0.02 0.20 0.45 0.2 0.03 0.01
[0048] Table 2 lists the technological parameters and mechanical properties in relation to the manufacturing of the superstrength cold ro||ed weathering steel sheet in Embodiments 1~7
[0049] Table 2 Heating and Coiling Reduction _ _ _ NO pfesefvi?g tempef few in iåílßâíålïïe Siïïåh Jïåšåfh Eblåítw" 23 ' temperature ature cold rolling bending (D) (D) (%) (Ci) (MPa) (MPa) (%) Embodiment 1A 1200 498 50 873 900 1043 8.4 passed Embodiment 1B 1180 457 60 880 1009 1117 6.7 passed Embodiment 1C 1180 546 60 854 841 1010 9.3 passed Embodiment 1D 1170 509 55 880 931 1067 7.3 passed Embodiment 2A 1190 550 55 859 763 1053 11 .1 passed Embodiment 2B 1170 508 60 879 851 1061 9.6 passed Embodiment 2C 1190 454 55 880 859 1162 9.1 passed Embodiment 2D 1200 482 60 862 762 1020 10.2 passed Embodiment 3A 1180 501 60 867 886 1162 8.6 passed 10 10 Embodiment 3B 1190 465 60 880 970 1231 8.4 passed Embodiment 3C 1180 534 55 871 749 1100 9.6 passed Embodiment 3D 1190 497 55 875 776 1114 10.8 passed Embodiment 4A 1170 495 55 880 903 1235 8.6 passed Embodiment 4B 1170 533 60 867 729 1154 10.3 passed Embodiment 4C 1180 514 55 872 854 1216 8.6 passed Embodiment 4D 1180 475 60 880 960 1231 8.2 passed Embodiment 5A 1190 523 60 878 940 1140 9.3 passed Embodiment 5B 1180 489 60 857 852 1067 11 passed Embodiment 5C 1190 550 60 865 861 1073 10.7 passed Embodiment 5D 1190 509 55 871 900 1173 9.8 passed Embodiment 6A 1200 497 60 848 825 1050 11.3 passed Embodiment 6B 1180 514 55 873 930 1211 8.9 passed Embodiment 6C 1170 506 55 864 900 1150 9.3 passed Embodiment 6D 1200 550 60 877 951 1198 9.6 passed Embodiment 7A 1200 526 55 880 856 1209 9.5 passed Embodiment 7B 1180 495 60 864 790 1120 11.5 passed Embodiment 7C 1200 487 55 858 807 1132 10.6 passed Embodiment 7D 1100 550 55 877 930 1220 9.4 passed
[0050] The compositions of the steel in Embodiments 1~7 in Table 2 corresponds to that in Table 1, that is, Embodiments 1A, 1B, 1C, and 1D all use the compositions in Embodiment 1 shown in Table 1.
[0051] in the present invention has a yield strength of more than 700Mpa, up to the Seen from Table 2, the superstrength cold rolled weathering steel sheet maximum of 1009 Mpa; a tensile strength of more than 1000Mpa, up to the maximum of 1235 Mpa; an elongation rate of more than 6%, up to the maximum of 11.5%; in the meantime, it has passed the 2a bending test. The steel sheet is adapted for manufacturing the parts like automobile structures and container panels with high strength and light weight, and the main forming processes of the finished steel sheets are rolling and simple folding, thereby having a broad application prospects _ 11
[0052] lt should be noted that the listed above are just some detailed embodiments of the present invention. Obviously, the present invention is limited to the above embodiments, and various modifications may be made with them. lf the skilled in the art conducts directly or associates any variations, all of them should fall within the protection scope of the claims.

Claims (15)

12 What is claimed is:
1. A superstrength cold rolled weathering steel sheet, wherein the weight percentage of the chemical elements thereof are as follows: C: 0.05~O.16%; Mn: 1.00~2.20%; Al: 0.02~0.06%; Cu: 0.20~0.40%; Cr: 0.40~0.60%; Ti: 0.015~0.035%; P: less than or equal to 0.03%; and C+Mn/16 is more than 0.19% and less than 0.23%; the remainders thereof being Fe and other unavoidable impurities.
2. The superstrength cold rolled weathering steel sheet according to Claim 1, wherein the weight percentage of the chemical elements thereof are further defined as follows: C: 0.07~0.15%; Mn: 1.30~2.00%; Al: 0.02~0.04%; Cu: 0.25~0.35%; P: less than or equal to O.15%.
3. The superstrength cold rolled weathering steel sheet according to Claim 2, wherein it further includes Ni of less than or equal to 0.20wt%.
4. The superstrength cold rolled weathering steel sheet according to Claim 1, wherein the microstructure thereof is martensite, the volume fraction of which is more than 95%.
5. The superstrength cold rolled weathering steel sheet according to Claim 1, wherein the thickness thereof is 0.8~1.5mm. 13
6. A container panel manufactured with said superstrength cold rolled weathering steel sheet according to any one of Claims 1 to 5.
7. An automobile structural plate manufactured with said superstrength cold rolled weathering steel sheet according to any one of Claims 1 to 5.
8. A method of manufacturing said superstrength cold rolled weathering steel sheet according to any one of Claims 1 to 5, wherein it comprises the following stages: smelting, heating and preservation, hot rolling, coiling, pickling, cold rolling, continuous annealing, skin passing; wherein, in the continuous annealing process, the annealing temperature is 830~880°C so as to enable the complete austenization, then the steel is cooled rapidly in an high hydrogen atmosphere so as to attain martensite structure.
9. The method of manufacturing said superstrength cold rolled weathering steel sheet according to Claim 8, wherein in the stage of continuous annealing, the volume fraction of hydrogen in the high hydrogen atmosphere is 60%.
10. The method of manufacturing said superstrength cold rolled weathering steel sheet according to Claim 8, wherein in the stage of continuous annealing, the cooling speed of the rapid cooling is more than 100°C/s.
11. The method of manufacturing said superstrength cold rolled weathering steel sheet according to Claim 8, wherein in the stage of continuous annealing, the annealing temperature is 850~880°C.
12. The method of manufacturing said superstrength cold rolled weathering steel sheet according to Claim 8, wherein in the stages of heating and preservation , the slab is heated and preserved at 1170~1200°C.
13. The method of manufacturing said superstrength cold rolled weathering steel sheet according to Claim 8, wherein in the stage of hot rolling, the finish rolling temperature is more than or equal to Ar3. 14
14. The method of manufacturing said superstrength cold rolled weathering steel sheet according to Claim 8, wherein in the stage of coiling, the coiling temperature is 450~550°C.
15. The method of manufacturing said superstrength cold rolled weathering steel sheet according to Claim 8, wherein in the stage of cold rolling, the reduction rate therein is 50~60%.
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