WO2018095258A1 - 一种高强耐蚀复合花纹钢及其制造方法 - Google Patents

一种高强耐蚀复合花纹钢及其制造方法 Download PDF

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WO2018095258A1
WO2018095258A1 PCT/CN2017/111252 CN2017111252W WO2018095258A1 WO 2018095258 A1 WO2018095258 A1 WO 2018095258A1 CN 2017111252 W CN2017111252 W CN 2017111252W WO 2018095258 A1 WO2018095258 A1 WO 2018095258A1
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strength
corrosion
substrate
resistant composite
steel
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PCT/CN2017/111252
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English (en)
French (fr)
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闫博
焦四海
夏小明
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宝山钢铁股份有限公司
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Priority to JP2019525766A priority Critical patent/JP6918941B2/ja
Priority to EP17873789.6A priority patent/EP3546611A4/en
Priority to AU2017364679A priority patent/AU2017364679B2/en
Priority to KR1020197013836A priority patent/KR20190072574A/ko
Publication of WO2018095258A1 publication Critical patent/WO2018095258A1/zh

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/38—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling sheets of limited length, e.g. folded sheets, superimposed sheets, pack rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B47/00—Auxiliary arrangements, devices or methods in connection with rolling of multi-layer sheets of metal
    • B21B47/02—Auxiliary arrangements, devices or methods in connection with rolling of multi-layer sheets of metal for folding sheets before rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B32B15/011—Layered products comprising a layer of metal all layers being exclusively metallic all layers being formed of iron alloys or steels
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C22C38/001—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
    • C22C38/02—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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/009—Pearlite
    • 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
    • C21D2251/00—Treating composite or clad material
    • C21D2251/02—Clad material
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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

Definitions

  • the invention relates to a composite board and a manufacturing method thereof, in particular to a composite pattern steel and a manufacturing method thereof.
  • the tread plate has the advantages of beautiful appearance and anti-slip surface, and thus is widely used in the market.
  • the pattern steel is divided into carbon steel tread plates and stainless steel tread plates.
  • the above pattern steels have the following problems:
  • the anti-corrosion treatment process is very expensive for production and labor costs, and it is not only highly demanding for the regional environment (for example, the anti-corrosion process needs to be carried out in an area with little dust), and the anti-corrosion material used is a chemical substance that is harmful to human health ( For example, anti-corrosion materials use paint).
  • the anti-corrosion treatment also affects the use of the steel plate.
  • the carbon steel tread plate also has a problem that the steel plate strength level is not high and the corrosion allowance is required to be increased, resulting in a large construction weight.
  • the stainless steel tread plate it has a problem of low yield strength and affects the overall stability of the member, and in order to meet the stability requirement of the member, the thickness of the stainless steel tread plate is increased during use, thereby affecting the weight of the member.
  • both the carbon steel tread plate and the stainless steel tread plate have problems of difficulty in welding.
  • the height of the pattern is the main indicator of the surface quality of the tread plate product. At present, it is difficult to meet the requirements for ensuring the height of the pattern in the prior art.
  • One of the objects of the present invention is to provide a high-strength and corrosion-resistant composite pattern steel, which has high strength, high corrosion resistance, yield strength ⁇ 470 MPa, and tensile strength by a composite rolling pattern by a reasonable chemical quality ratio. ⁇ 610MPa, shear strength ⁇ 410MPa, elongation ⁇ 40%.
  • the present invention provides a high-strength and corrosion-resistant composite pattern steel comprising a substrate and a patterned layer laminated on the substrate on one or both sides; the chemical element mass percentage of the substrate is:
  • the inevitable impurities are mainly S and P elements, and the lower the impurity element content, the better the technical effect, however, considering the actual steelmaking level of the steel mill, In the technical solution of the present invention, P ⁇ 0.015% and S ⁇ 0.010% in the control substrate.
  • Carbon is an austenite stabilizing element. It acts as a solid solution strengthening in steel, which can significantly increase the strength of steel.
  • the mass percentage of C is higher than 0.20%, it is detrimental to the weldability and toughness, and it is easy to increase the steel such as pearlite structure and Maao.
  • the hard phase structure of the island has an adverse effect on the corrosion resistance of steel. Therefore, considering the strength and toughness matching of the steel sheet and the corrosion resistance of the steel, the mass percentage of carbon in the substrate of the high-strength and corrosion-resistant composite pattern steel according to the present invention is controlled to be 0.01 to 0.20%, to ensure the The strength and toughness of the high-strength and corrosion-resistant composite pattern steel, and the welding performance is good.
  • Si In the technical solution of the present invention, adding silicon to steel can improve steel purity and deoxidation. Silicon acts as a solid solution strengthening in steel, but over-percentage of silicon is not conducive to soldering performance. Since the patterned double-layered steel also contains silicon, in the technical solution of the present invention, the mass percentage of silicon in the substrate is controlled to be 0.10-0.50%, and silicon in this range does not resist corrosion of the patterned layer. Sex has any effect and makes the substrate have good soldering properties.
  • Mn can delay pearlite transformation, reduce critical cooling rate, improve hardenability of steel, and have solid solution strengthening effect on steel, which is the main solid solution strengthening element in steel. .
  • the mass percentage of manganese is higher than 2.0%, the segregation zone and the martensite structure are likely to occur, which adversely affects the toughness of the steel.
  • the appearance of the segregation zone will also reduce the corrosion resistance of the steel.
  • the mass percentage of manganese is less than 0.5%, the strength level of the steel is not promoted. Therefore, the mass percentage of manganese in the substrate of the high-strength corrosion-resistant composite pattern steel according to the present invention is limited to 0.5-2.0%.
  • Al is a strong deoxidizing element in steel. In order to reduce the content of oxygen in the steel, the mass percentage of aluminum is controlled to be 0.02 to 0.04%. In addition, excess aluminum in the deoxidation and nitrogen in the steel can form AlN precipitates, which helps The strength of the high steel and the austenite grain size of the steel can be refined during heat treatment.
  • Ti is a strong carbide forming element.
  • the addition of a small amount of Ti in the steel is beneficial to the fixation of N in the steel.
  • the TiN formed can make the austenite grains of the base layer not excessively grow when the composite billet is heated, and refine the original austenite. Grain size.
  • Titanium may also be combined with carbon and sulfurized in steel to form TiC, TiS, Ti 4 C 2 S 2 , etc., and the above compounds exist in the form of inclusions and second phase particles.
  • the above carbonitride precipitates of titanium can also prevent grain growth in the heat-affected zone during soldering and improve soldering performance. Therefore, the mass percentage of titanium in the substrate of the high-strength and corrosion-resistant composite pattern steel according to the present invention is controlled to be 0.005 to 0.018%.
  • Nb: ⁇ is a strong carbide forming element.
  • ruthenium is added to the substrate mainly to increase the recrystallization temperature, so that the substrate grain is refined, which is advantageous for improving the low temperature impact toughness of the substrate. Therefore, the mass percentage of Nb according to the present invention is controlled to be 0.005 to 0.020%.
  • B Boron can greatly improve the hardenability of steel, can inhibit the formation of bainite, and in order to ensure high strength of the high-strength and corrosion-resistant composite pattern steel according to the present invention, the mass percentage of boron is controlled at: 0 ⁇ B ⁇ 0.0003%
  • N functions similarly to carbon, and the mass percentage of N is controlled at N ⁇ 0.006%, thereby ensuring the strength of the high-strength and corrosion-resistant composite pattern steel according to the present invention.
  • the mass percentage of N is preferably limited to N: 0.0005% to 0.005%.
  • the substrate further contains at least one of elements of Ni, Cr and Mo, wherein Ni ⁇ 0.20%, Cr ⁇ 0.20%, Mo ⁇ 0.10%.
  • Ni is added because: Ni is an element that stabilizes austenite and has a certain effect on improving the strength of steel.
  • the addition of nickel to steel, especially in quenched and tempered steel, can significantly increase the low temperature impact toughness of steel.
  • nickel is a precious alloying element, excessive addition increases production costs.
  • nickel in order to further improve the low-temperature impact toughness of the substrate, nickel may be added in an appropriate amount, and the mass percentage of Ni is controlled to be Ni ⁇ 0.20%.
  • Cr is added because: the segregation tendency of Cr is smaller than that of manganese.
  • the content of manganese can be appropriately reduced, and the reduced content is replaced by chromium, thereby increasing the strength of the steel and Corrosion resistance.
  • the addition of chromium to the substrate is also advantageous for suppressing the diffusion of chromium from the patterned layer to the substrate. Therefore, in the present invention, chromium may be appropriately added, and the mass percentage of Cr is controlled to be Cr ⁇ 0.20%.
  • Mo is added because: Mo can further refine grains and improve the strength and toughness of steel.
  • molybdenum can reduce the temper brittleness of the steel, and at the same time, it can precipitate very fine carbides during tempering, and significantly strengthen the matrix of the steel.
  • the addition of molybdenum is advantageous for suppressing the self-temper brittleness which is easily generated by the high-strength and corrosion-resistant composite pattern steel according to the present invention, but since molybdenum is a very expensive alloying element, the mass percentage of Mo in the technical solution of the present invention Limited to Mo ⁇ 0.10%.
  • the patterned layer is an austenitic stainless steel.
  • the austenitic stainless steel satisfying the requirements of national or international standards such as 304, 304L, 316, 316L, may be selected according to the specific conditions of each embodiment. .
  • the microstructure of the substrate is ferrite + pearlite.
  • a transition layer is provided at a joint of the substrate and the patterned layer, and the thickness of the transition layer is ⁇ 200 ⁇ m.
  • the mass percentage of each chemical element in the transition layer is a gradient distribution. That is to say, due to the difference in the mass ratio of the chemical layers in the patterned layer and the substrate, each chemical element diffuses from the side of higher mass percentage to the other side of lower mass percentage in the thickness direction to form a transition layer.
  • the transition layer is beneficial to improve the bonding strength between the substrate and the patterned layer, and is less likely to cause delamination cracking under plastic deformation during the formation of the pattern. Further, the transition layer promotes the metal element of the substrate to flow with the patterned layer metal. Conducive to the formation of the height of the pattern.
  • the thickness of the pattern composite layer accounts for 10-40% of the thickness of the high-strength corrosion-resistant composite pattern steel. This is because the thickness control of the pattern layer is beneficial to ensure the formability of the pattern, to ensure the corrosion resistance of the tread plate, and also to improve the mechanical properties of the steel.
  • the thickness of the pattern layer is greater than 40% of the thickness of the high-strength and corrosion-resistant composite pattern steel, the strength of the steel is affected; when the thickness of the pattern layer is less than 10% of the thickness of the high-strength corrosion-resistant composite pattern steel, the pattern layer cannot be rolled out. The higher pattern height reduces the surface quality and service life of the steel. Therefore, the thickness control of the pattern layer is advantageous for obtaining high corrosion resistance, mechanical properties and formability of the high-strength corrosion-resistant pattern steel according to the present invention.
  • the yield strength is ⁇ 470 MPa
  • the tensile strength is ⁇ 610 MPa
  • the shear strength is ⁇ 410 MPa
  • the elongation is ⁇ 40%.
  • Another object of the present invention is to provide a method for manufacturing the above high-strength corrosion-resistant composite pattern steel, comprising the steps of:
  • Composite rolling firstly, the composite is heated at a temperature of 1100 to 1180 ° C, and then multi-pass rolling is performed to obtain a composite steel plate, and the total reduction ratio is controlled to be not less than 70%, and the finish rolling temperature is not lower than 900 ° C, the last rolling of the multi-pass rolling surface pattern, control the final reduction rate of 10% -20%;
  • the high-strength and corrosion-resistant composite pattern steel is obtained by composite rolling, and the complete metallurgical bonding between the substrate and the composite layer is realized by controlling various parameters in the process, and the high-strength corrosion-resistant pattern obtained is obtained.
  • Steel has good corrosion resistance and excellent mechanical properties.
  • step (2) before the assembly of the substrate slab and the multi-layer slab, the surface of each layer requiring the bonding surface is pretreated to remove Surface oxide film.
  • the heating temperature of the preform is limited to 1100 to 1180 ° C because heating in this temperature range is advantageous for obtaining a uniform austenite structure of the laminated slab, so that the carbide is completely dissolved. Further, all or a part of the compound of the alloying element such as ruthenium or titanium in the substrate slab is dissolved, which is advantageous for complete metallurgical bonding.
  • the surface pattern is rolled by a pattern roll, and the pattern of the surface pattern can be set according to the specific conditions of the respective embodiments, such as a lenticular type or a rhombic shape.
  • the engraving depth of the pattern roll is set to 2.8-4 mm.
  • the finishing rolling temperature is controlled to be 920 to 1000 °C. This is because when the finish rolling temperature is higher than 1000 ° C, the steel sheet is likely to adhere to the pattern roll, resulting in filling in the pattern roll groove, so that the surface quality of the steel plate produced later cannot meet the requirements.
  • the coiling temperature is 500 to 650 °C. This is because when the coiling temperature is higher than 650 ° C, the surface pattern of the steel sheet will be imprinted on the adjacent strip surface when the coil is wound.
  • the high-strength and corrosion-resistant composite pattern steel according to the present invention has high strength and high corrosion resistance by the design of the substrate and the pattern layer, especially the control of the mass ratio of the chemical elements of the substrate, and the high-strength and corrosion-resistant composite
  • the pattern steel has a yield strength ⁇ 470 MPa, a tensile strength ⁇ 610 MPa, a shear strength ⁇ 410 MPa, and an elongation ⁇ 40%.
  • the high-strength and corrosion-resistant composite pattern steel according to the present invention has high surface quality and no cracking and delamination.
  • the manufacturing method of the high-strength and corrosion-resistant composite pattern steel according to the invention achieves the complete metallurgical combination of the substrate and the composite layer by controlling the various process parameters, so that the obtained high-strength and corrosion-resistant composite pattern steel also has the above advantages.
  • Fig. 1 shows the metallographic structure of the high-strength corrosion-resistant composite pattern steel of Example 1 under low power microscope observation.
  • Example 2 is a photograph of a metallographic structure of a substrate of the high-strength and corrosion-resistant composite pattern steel of Example 1.
  • Fig. 3 is a photograph showing the metallographic structure of the one-side transition layer between the substrate and the patterned layer of the high-strength and corrosion-resistant composite pattern steel of Example 1.
  • Fig. 5 is a schematic view showing the surface pattern of the pattern of the high-strength and corrosion-resistant composite pattern steel of Example 1.
  • Fig. 6 is a view showing the structure of the surface pattern in the pattern layer of the high-strength and corrosion-resistant composite pattern steel of Example 1 from another angle of view.
  • Table 1 lists the chemical element mass percentages of the respective green layers in the high-strength corrosion-resistant composite pattern steel of Examples 1-4.
  • the manufacturing method of the high-strength and corrosion-resistant composite pattern steel of Example 1-4 was prepared by the following steps (see Table 2 for the specific process parameters in each example):
  • Composite rolling firstly, the composite is heated at a temperature of 1100 to 1180 ° C, and then multi-pass rolling is performed to obtain a composite steel plate, and the total reduction ratio is controlled to be not less than 70%, and the final rolling temperature is 920- 1000 ° C, the last rolling of the surface of the multi-pass rolling, control the final reduction rate of 10% -20%;
  • the coiling temperature is 500-650 °C.
  • Table 2 lists the specific process parameters of the method for producing the high-strength corrosion-resistant composite pattern steel of Examples 1-4.
  • Table 3 lists the test results of the high-strength and corrosion-resistant composite pattern steels of Examples 1-4 after various performance tests.
  • Fig. 1 shows the metallographic structure of the high-strength corrosion-resistant composite pattern steel of Example 1 under low power microscope observation.
  • the high-strength and corrosion-resistant composite pattern steel of Example 1 has a pattern layer 1 and a substrate 2.
  • FIG. 2 is a photograph of a metallographic structure of a substrate of the high-strength and corrosion-resistant composite pattern steel of Example 1.
  • the substrate is a ferrite and a pearlite structure, and the microstructure grains are fine and uniform, and the average grain size of the ferrite is within 10 ⁇ m.
  • Fig. 3 is a photograph showing the metallographic structure of the one-side transition layer between the substrate and the patterned layer of the high-strength and corrosion-resistant composite pattern steel of Example 1.
  • the substrate 13 of the first embodiment has a transition layer 12 between the substrate layer 11 and the pattern layer 11.
  • FIG. 4 is a metallographic structure diagram of the other side transition layer between the substrate and the patterned layer of the high-strength and corrosion-resistant composite pattern steel of Example 1.
  • FIG. 4 the substrate 13 of the first embodiment has a transition layer 22 between the substrate layer 21 and the pattern layer 21.
  • the substrate of the first embodiment and the double-layer rolling composite layer on the substrate have a transition layer, and the formed transition layers 12 and 22 are favorable for improving the substrate 13 and the patterned layer 11,
  • the bonding strength of 21 makes the layer 1 less prone to delamination.
  • Fig. 5 is a schematic view showing the surface pattern of the pattern of the high-strength and corrosion-resistant composite pattern steel of Example 1. As shown in FIG. 5, the surface pattern of Example 1 was a lenticular shape.
  • Fig. 6 is a view showing the structure of the surface pattern in the pattern layer of the high-strength and corrosion-resistant composite pattern steel of Example 1 from another angle of view. As shown in Fig. 6, the surface pattern height h of Example 1 was 1.02 mm.

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Abstract

一种高强耐蚀复合花纹钢及其制造方法，包括基板和单面或双面轧制复合于基板上的花纹复层；该基板的化学元素质量百分比为：C：0.01～0.20％、Si：0.10～0.5％、Mn：0.5～2.0％、Al：0.02～0.04％、Ti：0.005～0.018％、Nb：0.005～0.020％、0＜B≤0.0003％、N≤0.006％，余量为铁和其他不可避免杂质。该高强耐蚀复合钢板强度高，耐蚀性强，其屈服强度≥470MPa，抗拉强度≥610MPa，剪切强度≥410MPa，延伸率≥40％。

Description

一种高强耐蚀复合花纹钢及其制造方法 技术领域
本发明涉及一种复合板及其制造方法，尤其涉及一种复合花纹钢及其制造方法。
背景技术
花纹板具有外形美观、表面防滑的优点，因而在市场应用广泛。目前花纹钢分为碳钢花纹板和不锈钢花纹板。然而上述花纹钢分别存在以下问题：
对于碳钢花纹板而言，在其长期使用过程中，由于碳钢锈蚀导致使用过程中存在安全隐患，因而，为了防止锈蚀而需要定期对花纹钢进行防腐处理。防腐处理过程对生产成本和人力成本耗费巨大，其不仅对于区域环境要求极高(例如防腐过程需要在灰尘极少的区域内进行)，而且所采用的防腐材料为对人体健康不利的化学物质(例如防腐材料使用油漆)。此外，对碳钢花纹板采用防腐处理时，防腐处理对钢板的使用也会造成影响。另外，碳钢花纹板还存在钢板强度级别不高、需要增加耐蚀裕量而造成构建重量偏大的问题。
对于不锈钢花纹板而言，其存在屈服强度低，影响构件整体稳定性的问题，而为了满足构件稳定性需求，在使用时，对不锈钢花纹板厚度增加，进而影响了构件重量。
此外，碳钢花纹板与不锈钢花纹板都存在焊接难度大的问题。
基于上述考虑，期望采用碳钢作为基层，提供结构性能例如强度，不锈钢板作为复层，提供耐蚀性，通过将基层与复层复合轧制成复合花纹钢，用以满足强度和耐蚀性的综合要求。
然而，目前现有技术在利用复合轧制实现复合花纹钢时存在如下技术难点：
(1)复合花纹板在轧制花纹时，花纹层金属向花纹辊刻槽内流动，复层与基层的结合面承受较大的拉应力，特别是花纹面复层的厚度较薄时，结合面容易分离、开裂。
(2)复合花纹板的复层与基层的物性参数、高温变形特性差别较大，从而使得轧制后的花纹板因末道次机架的负荷分配明显增大，导致生产不稳定，所产生的钢板表面质量不一。
(3)花纹高度是花纹板产品花纹表面质量的主要指标，目前现有技术中对保证花纹高度要求难以满足。
发明内容
本发明的目的之一在于提供一种高强耐蚀复合花纹钢，通过合理的化学质量配比使得采用复合轧制的复合花纹钢具有强度高，耐蚀性强，屈服强度≥470MPa，抗拉强度≥610MPa，剪切强度≥410MPa，延伸率≥40％。
为了实现上述目的，本发明提出了一种高强耐蚀复合花纹钢，包括基板和单面或双面轧制复合于基板上的花纹复层；所述基板的化学元素质量百分比为：
C：0.01～0.20％、Si：0.10～0.5％、Mn：0.5～2.0％、Al：0.02～0.04％、Ti：0.005～0.018％、Nb：0.005～0.020％、0＜B≤0.0003％、N≤0.006％，余量为铁和其他不可避免杂质。
在本发明所述的高强耐蚀复合花纹钢中，不可避免的杂质主要是S和P元素，杂质元素含量越低技术效果越好，然而考虑到钢厂的实际的炼钢水平，因而，在本发明技术方案中，控制基板中P≤0.015％，S≤0.010％。
本发明所述的高强耐腐蚀复合花纹钢中所述的基板的各化学元素的设计原理为：
C：碳是奥氏体稳定化元素。在钢中起到固溶强化的作用，能够明显提高钢的强度，然而当C的质量百分比高于0.20％时，则对焊接性能和韧性不利，也容易使钢增加诸如珠光体组织及马奥岛的硬相组织，对钢的耐蚀性能有不利影响。因此，综合考虑钢板的强韧性匹配以及对钢的耐蚀性的要求，本发明所述的高强耐蚀复合花纹钢的基板中的碳的质量百分比控制在0.01～0.20％，用以保证所述的高强耐蚀复合花纹钢的强度和韧性，且焊接性能良好。
Si：在本发明技术方案中，钢中加硅能提高钢质纯净度和脱氧。硅在钢中起固溶强化作用，但过高质量百分比的硅不利于焊接性能。由于花纹复层的钢中也含有硅，因而，在本发明技术方案中，对基板中的硅的质量百分比控制在0.10-0.50％，在此范围内的硅不会对花纹复层的耐蚀性有任何影响，且使得基板具备良好的焊接性能。
Mn：在本发明所述的技术方案中，Mn可以推迟珠光体转变，降低临界冷却速度，提高钢的淬透性，同时对钢具有固溶强化的作用，是钢中的主要固溶强化元素。但锰的质量百分比高于2.0％时，容易出现偏析带以及马氏体组织，对钢的韧性有不利影响。此外，偏析带的出现对钢的耐蚀性能也会有所降低。而当锰的质量百分比低于0.5％时，不利于钢的强度级别提升，因此，本发明所述的高强耐蚀复合花纹钢的基板中对锰的质量百分比限定在0.5-2.0％。
Al：Al是钢中的强脱氧元素。为了降低钢中的氧元素的含量，铝的质量百分比控制在0.02～0.04％。此外，脱氧后多余的铝和钢中的氮元素能形成AlN析出物，有助于提 高钢的强度并且在热处理加热时能细化钢的奥氏体晶粒度。
Ti：Ti是强碳化物形成元素，钢中加入微量的Ti有利于固定钢中的N，形成的TiN能使复合坯加热时基层奥氏体晶粒不过分长大，细化原始奥氏体晶粒度。钛在钢中还可分别与碳和硫化合生成TiC、TiS、Ti4C2S2等，上述化合物以夹杂物和第二相粒子的形式存在。钛的上述碳氮化物析出物在焊接时还可阻止热影响区晶粒长大，改善焊接性能。因此，本发明所述的高强耐蚀复合花纹钢中基板的钛的质量百分比控制在0.005～0.018％。
Nb：铌是强碳化物形成元素，在本发明所述的技术方案中，基板中加入铌主要是为了提高再结晶温度，使得基板晶粒细化，有利于基板的低温冲击韧性的提高。因此，本发明所述的Nb的质量百分比控制在0.005～0.020％。
B：硼能极大地提高钢的淬透性，可以抑制贝氏体的形成，为了保证本发明所述的高强耐蚀复合花纹钢具有高强度，因此，对硼的质量百分比控制在：0＜B≤0.0003％
N：在本发明所述的技术方案中，N起到的作用与碳相似，通过对N的质量百分比控制在N≤0.006％，从而保证本发明所述的高强耐蚀复合花纹钢强度。在一些优选的实施方式中，为了进一步保证所述的高强耐蚀复合花纹钢的强度，对N的质量百分比优选限定在N：0.0005％～0.005％。
进一步地，本发明所述的高强耐蚀复合花纹钢中，所述基板还含有Ni、Cr和Mo元素的至少其中之一，其中Ni≤0.20％、Cr≤0.20％、Mo≤0.10％。
其中，添加Ni是因为：Ni是稳定奥氏体的元素，对提高钢的强度有一定的作用。钢中加镍，尤其是在调质钢中加镍能大幅提高钢的低温冲击韧性。但是由于镍属于贵重合金元素，添加过多会增加生产成本。对于本发明所述的技术方案而言，为了进一步提高基板的低温冲击韧性的时，可适量添加镍，Ni的质量百分比控制在Ni≤0.20％。
添加Cr是因为：Cr的偏析倾向较锰小，当基板的钢中有明显的偏析带及带状组织的时候，可适当降低锰的含量，减少的含量以铬替代，从而提高钢的强度和耐蚀性。此外，基板中添加铬也有利于抑制花纹复层的铬向基板扩散。因此，在本发明中可适量添加铬，Cr的质量百分比控制在Cr≤0.20％。
添加Mo是因为：Mo能进一步细化晶粒，提高钢的强度和韧性。在本发明技术方案中，钼能减少钢的回火脆性，同时回火时还能析出非常细小的碳化物，显著强化钢的基体。此外，钼的添加有利于抑制本发明所述的高强耐蚀复合花纹钢容易产生的自回火脆性，但由于钼是非常昂贵的合金元素，因此，本发明的技术方案中对Mo的质量百分比 限定在Mo≤0.10％。
进一步地，本发明所述的高强耐蚀复合花纹钢中，所述花纹复层为奥氏体不锈钢。
需要说明的是，在本发明所述的高强耐蚀复合花纹钢中花纹复合层可以根据各实施方式的具体情况选择满足国家或国际标准要求的奥氏体不锈钢，例如304、304L、316、316L。
进一步地，本发明所述的高强耐蚀复合花纹钢中，所述基板的微观组织为铁素体+珠光体。
进一步地，本发明所述的高强耐蚀复合花纹钢中，在基板和花纹复层的结合处具有过渡层，所述过渡层的厚度≤200μm。
所述的过渡层中各化学元素质量百分比呈梯度分布。也就是说，由于花纹复层和基板中各化学元素质量配比的不同，因此，各化学元素沿厚度方向从质量百分比较高的一侧扩散至质量百分比较低的另一侧，形成过渡层中各元素梯度分布。所述的过渡层有利于提高基板与花纹复层的结合强度，在花纹形成过程中的塑性变形下不易发生分层开裂，此外，所述的过渡层促进基板金属元素随花纹复层金属流动，有利于花纹高度的形成。
进一步地，本发明所述的高强耐蚀复合花纹钢中，花纹复层的厚度占高强耐蚀复合花纹钢厚度的10-40％。这是因为：对花纹复层的厚度控制有利于保证花纹的成形性、保证花纹板的耐蚀性，并且还有利于提升钢力学性能。当花纹复层的厚度大于高强耐蚀复合花纹钢厚度的40％，则影响钢的强度；当花纹复层的厚度小于高强耐蚀复合花纹钢厚度的10％，则花纹复层无法轧制出较高的花纹高度，降低了钢的表面质量和使用寿命。因此，对花纹复层的厚度控制有利于本发明所述的高强耐蚀花纹钢获得良好的耐蚀性能、力学性能及成形性。
进一步地，本发明所述的高强耐蚀复合花纹钢中，其屈服强度≥470MPa，抗拉强度≥610MPa，剪切强度≥410MPa，延伸率≥40％。
相应地，本发明的另一目的还在于提供一种上述高强耐蚀复合花纹钢的制造方法，包括步骤：
(1)制得基板板坯和复层板坯；
(2)将基板板坯和复层板坯进行组坯，对各层的贴合面的四周进行焊接密封，然后抽真空；
(3)复合轧制：先将组坯在1100～1180℃的温度下加热，然后进行多道次轧制，得到复合钢板，控制总压下率不低于70％，终轧温度不低于900℃，多道次轧制的最后一道次轧制表面花纹，控制最后一道次的压下率为10％-20％；
(4)水冷后卷取。
在本发明所述的制造方法中，采用复合轧制获得高强耐蚀复合花纹钢，通过对工艺中各参数的控制实现了基板与复层之间的完全冶金结合，所获得的高强耐蚀花纹钢兼具良好的耐蚀性和优良的力学性能。
需要说明的是，在一些优选的实施方式中，在步骤(2)中，对基板板坯和复层板坯的组坯前，对各层的需要贴合面的表面进行预处理，以去除表面氧化膜。
此外，在步骤(3)中，组坯加热温度限定在1100～1180℃，是因为：在此温度范围内加热，有利于复层板坯获得均匀的奥氏体组织，使得碳化物完全溶解，并且使得基板板坯中的铌、钛等合金元素的化合物全部或部分溶解，有利于完全冶金结合。
另外，在本发明所述的技术方案中，表面花纹采用花纹辊轧制，表面花纹的样式可根据各实施方式的具体情况进行设置，例如扁豆型、菱形。为了进一步提高表面花纹的质量，花纹辊刻花深度设置为2.8-4mm。
进一步地，本发明所述的制造方法中，在所述步骤(3)中，控制终轧温度为920-1000℃。这是因为，当终轧温度高于1000℃时，易出现钢板粘结在花纹辊上，导致花纹辊槽内内填充，使得之后生产的钢板表面花纹质量无法达到要求。
进一步地，本发明所述的制造方法中，在所述步骤(4)中，卷取温度为500～650℃。这是因为：当卷取温度高于650℃时，成卷时钢板表面花纹会刻印在相邻的带钢表面。
本发明所述的高强耐蚀复合花纹钢通过基板和花纹复层的设计，尤其是对基板各化学元素质量比的控制，使其具有高强度和高耐蚀性能，所述的高强耐蚀复合花纹钢，其屈服强度≥470MPa，抗拉强度≥610MPa，剪切强度≥410MPa，延伸率≥40％。
此外，本发明所述的高强耐蚀复合花纹钢表面质量高，无开裂分层现象。
本发明所述的高强耐蚀复合花纹钢的制造方法通过对各工艺参数的控制，实现了基板与复层的完全冶金结合，使得所获得的高强耐蚀复合花纹钢也具有上述优点。
附图说明
图1显示了实施例1的高强耐蚀复合花纹钢在低倍镜观察下的金相组织。
图2为实施例1的高强耐蚀复合花纹钢的基板的金相组织照片。
图3为实施例1的高强耐蚀复合花纹钢的位于基板与花纹复层间的一侧过渡层的金相组织照片。
图4为实施例1的高强耐蚀复合花纹钢的位于基板与花纹复层间的另一侧过渡层的金 相组织图。
图5为实施例1的高强耐蚀复合花纹钢的花纹复层中表面花纹样式示意图。
图6显示了实施例1的高强耐蚀复合花纹钢的花纹复层中表面花纹在另一视角下的结构示意图。
具体实施方式
下面将结合说明书附图和具体的实施例对本发明所述的一种高强耐蚀复合花纹钢及其制造方法做进一步的解释和说明，然而该解释和说明并不对本发明的技术方案构成不当限定。
实施例1-4
表1列出了实施例1-4的高强耐蚀复合花纹钢中各坯层的化学元素质量百分比。
表1.(wt％，余量为Fe和除了P、S以外其他不可避免的杂质)
Figure PCTCN2017111252-appb-000001
实施例1-4的高强耐蚀复合花纹钢的制造方法采用以下步骤制得(各实施例中的具体工艺参数参见表2)：
(1)按照表1所列的各化学组分制得基板板坯和复层板坯；
(2)将基板板坯和复层板坯进行组坯，对各层的贴合面的四周进行焊接密封，然后抽真空；
(3)复合轧制：先将组坯在1100～1180℃的温度下加热，然后进行多道次轧制，得到复合钢板，控制总压下率不低于70％，终轧温度为920-1000℃，多道次轧制的最后一道次轧制表面花纹，控制最后一道次的压下率为10％-20％；
(4)水冷后卷取，卷取温度为500-650℃。
表2列出了实施例1-4的高强耐蚀复合花纹钢的制造方法的具体工艺参数。
表2.
Figure PCTCN2017111252-appb-000002
表3列出了实施例1-4的高强耐蚀复合花纹钢经各项性能测试后的测试结果。
表3.
Figure PCTCN2017111252-appb-000003
由表3可以看出，实施例1-4的屈服强度≥470MPa，抗拉强度≥610MPa，剪切强度≥410MPa，延伸率≥40％，说明本案各实施例的强度较高，力学性能优良。
图1显示了实施例1的高强耐蚀复合花纹钢在低倍镜观察下的金相组织。如图1所示，实施例1的高强耐蚀复合花纹钢具有花纹复层1和基板2。
图2为实施例1的高强耐蚀复合花纹钢的基板的金相组织照片。如图2所示，基板为铁素体和珠光体组织，微观组织晶粒细小、均匀，铁素体平均晶粒尺寸在10μm以内。
图3为实施例1的高强耐蚀复合花纹钢的位于基板与花纹复层间的一侧过渡层的金相组织照片。如图3所示，实施例1的基板13与花纹复层11间具有过渡层12。
图4为实施例1的高强耐蚀复合花纹钢的位于基板与花纹复层间的另一侧过渡层的金相组织图。如图4所示，实施例1的基板13与花纹复层21间具有过渡层22。
结合图3和图4可知，实施例1的基板和双面轧制复合于基板上的花纹复层间具有过渡层，所形成的过渡层12和22有利于提高基板13与花纹复层11、21的结合强度，使得实施例1不易发生分层开裂。
图5为实施例1的高强耐蚀复合花纹钢的花纹复层中表面花纹样式示意图。如图5所示，实施例1的表面花纹样式为扁豆形。
图6显示了实施例1的高强耐蚀复合花纹钢的花纹复层中表面花纹在另一视角下的结构示意图。如图6所示，实施例1的表面花纹高度h为1.02mm。
需要注意的是，以上列举的仅为本发明的具体实施例，显然本发明不限于以上实施例，随之有着许多的类似变化。本领域的技术人员如果从本发明公开的内容直接导出或联想到的所有变形，均应属于本发明的保护范围。

Claims (10)

  1. 一种高强耐蚀复合花纹钢，其特征在于，包括基板和单面或双面轧制复合于基板上的花纹复层；所述基板的化学元素质量百分比为：
    C：0.01～0.20％、Si：0.10～0.5％、Mn：0.5～2.0％、Al：0.02～0.04％、Ti：0.005～0.018％、Nb：0.005～0.020％、0＜B≤0.0003％、N≤0.006％，余量为铁和其他不可避免杂质。
  2. 如权利要求1所述的高强耐蚀复合花纹钢，其特征在于，所述基板还含有Ni、Cr和Mo元素的至少其中之一，其中Ni≤0.20％、Cr≤0.20％、Mo≤0.10％。
  3. 如权利要求1所述的高强耐蚀复合花纹钢，其特征在于，所述花纹复层为奥氏体不锈钢。
  4. 如权利要求1所述的高强耐蚀复合花纹钢，其特征在于，所述基板的微观组织为铁素体+珠光体。
  5. 如权利要求1所述的高强耐蚀复合花纹钢，其特征在于，在基板和花纹复层的结合处具有过渡层，所述过渡层的厚度≤200μm。
  6. 如权利要求1所述的高强耐蚀复合花纹钢，其特征在于，花纹复层的厚度占高强耐蚀复合花纹钢厚度的10-40％。
  7. 如权利要求1-6中任意一项所述的高强耐蚀复合花纹钢，其屈服强度≥470MPa，抗拉强度≥610MPa，剪切强度≥410MPa，延伸率≥40％。
  8. 如权利要求1-7中任意一项所述的高强耐蚀复合花纹钢的制造方法，其特征在于，包括步骤：
    (1)制得基板板坯和复层板坯；
    (2)将基板板坯和复层板坯进行组坯，对各层的贴合面的四周进行焊接密封，然后抽真空；
    (3)复合轧制：先将组坯在1100～1180℃的温度下加热，然后进行多道次轧制，得 到复合钢板，控制总压下率不低于70％，终轧温度不低于900℃，多道次轧制的最后一道次轧制表面花纹，控制最后一道次的压下率为10％-20％；
    (4)水冷后卷取。
  9. 如权利要求8所述的制造方法，其特征在于，在所述步骤(3)中，控制终轧温度为920-1000℃。
  10. 如权利要求8所述的制造方法，其特征在于，在所述步骤(4)中，卷取温度为500～650℃。
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