WO2012022184A1 - Hot-dip galvanized high strength steel with high strain hardening index and method producing same - Google Patents
Hot-dip galvanized high strength steel with high strain hardening index and method producing same Download PDFInfo
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- WO2012022184A1 WO2012022184A1 PCT/CN2011/075236 CN2011075236W WO2012022184A1 WO 2012022184 A1 WO2012022184 A1 WO 2012022184A1 CN 2011075236 W CN2011075236 W CN 2011075236W WO 2012022184 A1 WO2012022184 A1 WO 2012022184A1
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- temperature
- hot
- dip galvanized
- strength steel
- cooling
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 61
- 239000010959 steel Substances 0.000 title claims abstract description 61
- 238000005482 strain hardening Methods 0.000 title claims description 21
- 238000000034 method Methods 0.000 title claims description 9
- 238000001816 cooling Methods 0.000 claims abstract description 43
- 238000005246 galvanizing Methods 0.000 claims abstract description 26
- 238000005096 rolling process Methods 0.000 claims abstract description 26
- 238000010438 heat treatment Methods 0.000 claims abstract description 18
- 238000003723 Smelting Methods 0.000 claims abstract description 17
- 238000005097 cold rolling Methods 0.000 claims abstract description 10
- 238000009749 continuous casting Methods 0.000 claims abstract description 10
- 239000010960 cold rolled steel Substances 0.000 claims abstract description 9
- 239000012535 impurity Substances 0.000 claims abstract description 9
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 11
- 239000000203 mixture Substances 0.000 claims description 11
- 239000000758 substrate Substances 0.000 claims description 11
- 229910052725 zinc Inorganic materials 0.000 claims description 11
- 239000011701 zinc Substances 0.000 claims description 11
- 230000009467 reduction Effects 0.000 claims description 9
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 8
- 229910052782 aluminium Inorganic materials 0.000 claims description 8
- 238000007654 immersion Methods 0.000 claims description 7
- 238000007747 plating Methods 0.000 claims description 7
- 239000007788 liquid Substances 0.000 claims description 4
- 238000004519 manufacturing process Methods 0.000 abstract description 13
- 238000003466 welding Methods 0.000 abstract description 7
- 230000007797 corrosion Effects 0.000 abstract description 6
- 238000005260 corrosion Methods 0.000 abstract description 6
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 abstract 2
- 229910052742 iron Inorganic materials 0.000 abstract 1
- 238000004804 winding Methods 0.000 abstract 1
- 229910001566 austenite Inorganic materials 0.000 description 22
- 239000000463 material Substances 0.000 description 14
- 230000000717 retained effect Effects 0.000 description 14
- 229910001335 Galvanized steel Inorganic materials 0.000 description 7
- 239000008397 galvanized steel Substances 0.000 description 7
- 238000005728 strengthening Methods 0.000 description 7
- 229910000794 TRIP steel Inorganic materials 0.000 description 6
- 230000000694 effects Effects 0.000 description 6
- 230000015572 biosynthetic process Effects 0.000 description 4
- 229910000734 martensite Inorganic materials 0.000 description 4
- 230000009466 transformation Effects 0.000 description 4
- 229910001567 cementite Inorganic materials 0.000 description 3
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 3
- 230000008569 process Effects 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- 229910004283 SiO 4 Inorganic materials 0.000 description 2
- 230000002411 adverse Effects 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 229910052758 niobium Inorganic materials 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910000746 Structural steel Inorganic materials 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 125000004432 carbon atom Chemical group C* 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000007812 deficiency Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000001627 detrimental effect Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 238000011056 performance test Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 229910052814 silicon oxide Inorganic materials 0.000 description 1
- 238000002791 soaking Methods 0.000 description 1
Classifications
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
- C21D6/002—Heat treatment of ferrous alloys containing Cr
-
- 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
- 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
- C22C38/18—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
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
- C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
- C23C2/0224—Two or more thermal pretreatments
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/26—After-treatment
- C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
- C23C2/29—Cooling or quenching
Definitions
- the invention relates to a galvanized steel, in particular to a hot-dip galvanized high-strength steel, specifically, a strain hardening index, that is, an n value exceeding 0.230, a yield strength of 400-450 MPa, and a tensile strength of not less than 600 MPa.
- a hot-dip galvanized steel sheet having an elongation of not less than 28% and a production method thereof.
- High-strength, high-plastic hot-dip galvanized steel sheet can be used to manufacture automotive structural parts, improve vehicle safety, and at the same time increase corrosion resistance, reduce steel sheet thickness by more than 20%, reduce total vehicle weight, reduce material consumption, and reduce fuel consumption. Consumption and exhaust emissions, and vigorous development of high-strength steel is an important method for car lightweighting.
- TRIP steel induces martensite nucleation under the plastic deformation of residual austenite in the steel sheet by phase transformation induced plasticity effect.
- Phase transformation strengthening and plastic growth, improving the strength and toughness of the steel sheet the steel has high yield strength and tensile strength, strong ductility and high stamping forming ability.
- As a structural component of an automobile it can reduce the weight of the automobile, enhance the impact resistance of the automobile, and has good formability, rigidity, collision energy absorbing ability, and weldability.
- a typical CMnSi-based TRIP steel contains 0.1 to 0.2% C, 1% to 2% Mn, and 1% to 2% Si, and is subjected to hot rolling deformation heat treatment or cold rolling + heat treatment.
- the structure of TRIP steel consists of 50% to 60% ferrite, 25% to 40% bainite or a small amount of martensite and 5% to 15% retained austenite.
- the surface of the TRIP steel is liable to form an oxide of Si, causing serious surface defects, so the wettability is poor, and there is a bottleneck of poor galvanizing adhesion property, and it is difficult to achieve the corrosion resistance of the hot-dip galvanized steel sheet.
- the chemical composition of the substrate is known from the patent document No. 200810119818, entitled "A TRIP steel sheet for high-strength cold-rolled hot-dip galvanizing and its preparation method”. %) is C: 0.1 to 0.4, Si ⁇ 0.06, Mn: 0.5 to 2.5, Al: 0.5 to 2.0, P ⁇ 0.03, S ⁇ 0.02, Nb: 0.01 to 0.10, Ti: 0.01 to 0.10, Cu: 0.1 to 1.0 Ni: 0.1 ⁇ 0.6, the balance is Fe.
- the steel plate introduced in this document is made of Nb and Ti microalloyed, and other strengthening elements such as Cu and Ni are added. The deficiency of its existence: 0.54% of Cu element is added in the embodiment.
- the purpose of the invention is to overcome the shortcomings such as the drawing property and the poor galvanizing performance, and provide a zinc layer of the galvanized steel sheet with good adhesion by changing the chemical composition and the production process, and the strain hardening index is not low.
- a hot-dip galvanized steel sheet having a yield strength of 400 to 450 MPa, a tensile strength of not less than 600 MPa, and an elongation of not less than 28% at 0.23 and a production method thereof.
- High-strain hardening index of hot-dip galvanized high-strength steel the composition and weight percentage of the substrate are: C: 0.11 ⁇ 0.20, Al: 0.51 ⁇ 1.22, Mn: 1.50 ⁇ 2.00, Si: 0.07 ⁇ 0.30, Cr: 1.0 ⁇ 2.0 , P ⁇ 0.015, S ⁇ 0.015, the balance is Fe and unavoidable impurities.
- the method further comprises: adding one or more of weight percentages: Nb: 0.10 to 0.20, Mo: 0.01 to 0.05, and V: 0.01 to 0.05.
- a method for producing a high strain hardening index of hot-dip galvanized high-strength steel the steps of which:
- the cold rolled steel plate is heated to 780 ⁇ 798 ° C;
- the zinc liquid contains aluminum in a weight percentage of 0.20 to 0.24.
- C is an austenite stability element, and its price is low. At the same time, C is also a gap strengthening element, and the strengthening effect is very obvious. The higher the C content, the better the strengthening effect. However, the C content is too high, which is not conducive to ensuring the welding performance of the material. In addition to increasing the strength, C plays a crucial role in the improvement of plasticity in the present invention. At high temperature, C can be dissolved in the retained austenite to improve the stability of the retained austenite. By controlling the cooling, a moderately stable retained austenite is obtained at room temperature. Residual austenite undergoes a structural transformation under external force and transforms into martensite, which can increase the strength of the material. Therefore, the upper limit of the C content is controlled to 0.20% or less, and the lower limit is controlled to be 0.11% or more.
- Al At present, conventional high-strength steel mostly increases the quantity and stability of retained austenite by adding Si element, and inhibits the formation of cementite.
- Si element easily forms a dense oxide layer Mn 2 SiO 4 on the surface of the steel sheet, thus affecting The galvanizing properties of the material, so the present invention uses Al instead of most of the Si.
- Al like Si, has fine grain and stabilized retained austenite to inhibit the formation of cementite.
- Al is a non-carbide forming element that promotes the diffusion of carbon atoms from ferrite into austenite. Thereby increasing the amount and stability of retained austenite. Al is prone to block the nozzle during continuous casting in industrial production. Therefore, the upper limit of Al element in steel is controlled to be less than 1.22%.
- Si:Si further refines grains and stabilizes retained austenite, and compensates for the lack of retained austenite and insufficient stability due to insufficient Al content.
- Si element also strengthens the steel substrate. effect.
- the Si element easily forms a dense oxide layer Mn 2 SiO 4 on the surface of the steel sheet, thereby affecting the galvanizing performance of the material, it is limited to 0.07 to 0.30%.
- Mn element is a conventional strengthening and toughening element.
- austenite forming element “not only can expand the austenite region, lower the finishing temperature, delay the transformation of austenite, but also refine grains and stabilize at the same time. The role of retained austenite.
- the content of Mn is too high, on the one hand, the cost is increased, on the other hand, the hardenability of the steel is increased, and the hardened layer of the welded structure causes the crack weld and the crack sensitivity of the heat-affected zone to be increased.
- the upper limit of the Mn content is controlled to 2.0% or less, and the lower limit is controlled to 1.50% or more.
- Cr is a ferrite forming element, and Cr element can significantly increase the strength of steel, and compensates for the adverse effect of the strength reduction caused by Al instead of Si in the present invention, and at the same time, Cr element can improve the oxidation resistance and resistance of steel. Corrosive. The Cr content is too low, the strength of the steel sheet is insufficient, and the steel sheet costs are too high, which also affects the overall performance of the steel sheet, so the Cr is controlled within the range of 1.0 to 2.0%.
- S:S is disadvantageous to the plastic toughness of the material of the present invention, and the corrosion resistance is lowered, so the lower the better.
- P:P is detrimental to the plasticity, weldability and formability of the material of the present invention, so the lower the better.
- Nb and Ti are strong carbonitride forming elements, which are favorable for precipitation strengthening, and can prevent high temperature austenite from growing excessively, but the Nb content is too high, which tends to cause carbonitride segregation, and the processability thereof is deteriorated. , increased material costs.
- Mo refines the grain of steel and maintains sufficient strength and creep resistance at high temperatures.
- V:V can suppress the formation of pearlite or cementite when it is rapidly cooled from the annealing temperature. At the same time, V can improve strength and toughness, and can also improve hydrogen corrosion resistance.
- the invention solves the problem that the traditional high Si content high strength steel has difficulty in galvanizing, has good platability, high drawing property, good welding performance, high corrosion resistance and good forming performance, and reflects It has a good market application prospect and significant social and economic benefits.
- the use of the material of the invention has the following advantages:
- the invention contains more than 7% of retained austenite.
- the retained austenite is transformed into martensite by absorbing external energy, so that the material not only exhibits good elongation and drawability.
- the strength of the material is further improved, and the size of the part after deformation is kept stable due to the release of the bending deformation stress.
- the invention material contains stable retained austenite.
- the retained austenite can absorb the crack tip stress and alleviate the crack formation and expansion. Therefore, no cracks and cracks occur during the welding of the parts, and the welding is good. performance.
- the invention material is excellent in ensuring the basic mechanical properties, and is excellent in the galvanizing property by the reasonable chemical composition and galvanizing process of the invention, not only has high strength and high drawability, but also has resistance. Corrosive, it is the ideal structural steel plate for high-end cars.
- Example 1 Hot-dip galvanized high-strength steel with high strain hardening index, the composition and weight percentage of the substrate were: C: 0.15, Al: 1.00, Mn: 1.76, Si: 0.15, Cr: 1.50, P: 0.012, S : 0.010, Nb: 0.10, the balance is Fe and unavoidable impurities.
- a method for producing a high strain hardening index of hot-dip galvanized high-strength steel the steps of which:
- control the rough rolling temperature is 1110 ⁇ 1120 ° C;
- the cold rolled steel plate is heated to 792 ⁇ 798 ° C, heating time is 220 seconds;
- Example 2 Hot-dip galvanized high-strength steel with high strain hardening index, the composition and weight percentage of the substrate were: C: 0.15, Al: 1.10, Mn: 1.75, Si: 0.21, Cr: 1.26, P: 0.015, S : 0.009, the balance is Fe and unavoidable impurities.
- a method for producing a high strain hardening index of hot-dip galvanized high-strength steel the steps of which:
- Smelting is carried out under the condition of a vacuum degree of 67 Pa, and the smelting temperature is controlled to be 1600 to 1610 ° C, and continuously cast into a billet;
- control the rough rolling temperature is 1090 ⁇ 1105 ° C;
- the cold rolled steel plate is heated to 785 ⁇ 795 ° C, the heating time is 210 seconds;
- Example 3 Hot-dip galvanized high-strength steel with high strain hardening index, the composition and weight percentage of the substrate were: C: 0.11, Al: 1.22, Mn: 1.55, Si: 0.07, Cr: 1.0, P: 0.013, S : 0.008, the balance is Fe and unavoidable impurities.
- a method for producing a high strain hardening index of hot-dip galvanized high-strength steel the steps of which:
- Smelting is carried out under the condition of a vacuum degree of 80 Pa, and the smelting temperature is controlled to be 1590 to 1595 ° C, and continuously cast into a billet;
- the cold rolled steel plate is heated to 780 ⁇ 785 ° C, heating time is 200 seconds;
- Example 4 Hot-dip galvanized high-strength steel with high strain hardening index, the composition and weight percentage of the substrate are: C: 0.20, Al: 0.50, Mn: 2.0, Si: 0. 30, Cr: 1.20, P: 0.009, S: 0.008, Mo: 0.01, the balance being Fe and unavoidable impurities.
- a method for producing a high strain hardening index of hot-dip galvanized high-strength steel the steps of which:
- Smelting is carried out under the condition of a vacuum degree of 134 Pa, and the smelting temperature is controlled to be 1600 to 1610 ° C, and continuously cast into a billet;
- control the rough rolling temperature is 1090 ⁇ 1100 ° C;
- the cold rolled steel plate is heated to 785 ⁇ 790 ° C, heating time is 220 seconds;
- Example 5 Hot-dip galvanized high-strength steel with high strain hardening index, the composition and weight percentage of the substrate were: C: 0.16, Al: 0.94, Mn: 1.52, Si: 0.22, Cr: 2.0, P: 0.011, S : 0.010, Mo: 0.05, V: 0.01, the balance being Fe and unavoidable impurities.
- a method for producing a high strain hardening index of hot-dip galvanized high-strength steel the steps of which:
- Smelting is carried out under the condition of a vacuum degree of 80 Pa, and the smelting temperature is controlled to be 1620 to 1630 ° C, and continuously cast into a billet;
- control the rough rolling temperature is 1110 ⁇ 1120 ° C;
- the cold rolled steel plate is heated to 792 ⁇ 798 ° C, heating time is 200 seconds;
- Example 6 Hot-dip galvanized high-strength steel with high strain hardening index, the composition and weight percentage of the substrate were: C: 0.15, Al: 1.05, Mn: 1.55, Si: 0.18, Cr: 1.10, P: 0.008, S : 0.006, Mo: 0.01, V: 0.05, Nb: 0.20, the balance being Fe and unavoidable impurities.
- a method for producing a high strain hardening index of hot-dip galvanized high-strength steel the steps of which:
- the cold rolled steel plate is heated to 780 ⁇ 790 ° C, the heating time is 210 seconds;
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Abstract
A hot-dip galvanized high strength steel consists of (wt.%): C:0.11-0.20,Al:0.51-1.22,Mn:1.50-2.00,Si:0.07-0.30,Cr:1.0-2.0,P≤0.015,S≤0.015, and the balance of iron and unavoidable impurities. A method for producing the same comprises the following steps: smelting and continuous casting into billet; heating the continuous cast billet and preserving heat; rough rolling; final rolling; winding up; cold rolling; and hot-dip galvanizing, i.e. heating the cold rolled steel plate, preserving heat, rapid cooling to the temperature of 480-510℃, dip galvanizing for 5-9 seconds, and then cooling to room temperature. The hot-dip galvanized high strength steel has the characteristics of good galvanizability, high tensile property and good welding performance, corrosion resistance and formability.
Description
本发明涉及一种镀锌钢,具体属于热镀锌高强度钢,确切地说,是一种应***化指数即n值超过0.230,屈服强度为400~450MPa,抗拉强度为不低于600MPa,延伸率不低于28%的热镀锌钢板及其生产方法。
The invention relates to a galvanized steel, in particular to a hot-dip galvanized high-strength steel, specifically, a strain hardening index, that is, an n value exceeding 0.230, a yield strength of 400-450 MPa, and a tensile strength of not less than 600 MPa. A hot-dip galvanized steel sheet having an elongation of not less than 28% and a production method thereof.
高强度、高塑性热镀锌钢板可用于制造汽车结构件,提高汽车安全性,同时,也增加耐腐蚀性,可减少钢板厚度20%以上,降低汽车总重量,既减少材料消耗,又降低燃料消耗及废气排放,大力发展高强钢是汽车轻量化的重要方法。High-strength, high-plastic hot-dip galvanized steel sheet can be used to manufacture automotive structural parts, improve vehicle safety, and at the same time increase corrosion resistance, reduce steel sheet thickness by more than 20%, reduce total vehicle weight, reduce material consumption, and reduce fuel consumption. Consumption and exhaust emissions, and vigorous development of high-strength steel is an important method for car lightweighting.
近年来,对于抗拉强度超过600MPa的高强度钢板的成形性能要求越来越高,TRIP钢是通过相变诱导塑性效应使钢板中残余奥氏体在塑性变形作用下诱发马氏体形核,引入相变强化和塑性增长,提高钢板的强度和韧性,该钢种具有高的屈服强度和抗拉强度,延展性强,冲压成形能力高。作为汽车结构部件可减轻汽车重量、增强汽车抗冲击能力,具有良好的成形性、刚性、碰撞能量吸收能力、焊接性。典型CMnSi系TRIP钢含0.1~0.2%C,1%~2%Mn,1%~2%Si,通过热轧变形热处理或冷轧+热处理。TRIP钢的组织由50%~60%铁素体、25%~40%贝氏体或少量马氏体和5%~15%残余奥氏体组成。然而,这种TRIP钢表面易形成Si的氧化物,造成严重的表面缺陷,所以浸润性很差,存在镀锌附着性能差的瓶颈,难以达到热镀锌钢板的耐腐蚀性目的。In recent years, the forming performance requirements of high-strength steel sheets with tensile strength exceeding 600 MPa are getting higher and higher. TRIP steel induces martensite nucleation under the plastic deformation of residual austenite in the steel sheet by phase transformation induced plasticity effect. Phase transformation strengthening and plastic growth, improving the strength and toughness of the steel sheet, the steel has high yield strength and tensile strength, strong ductility and high stamping forming ability. As a structural component of an automobile, it can reduce the weight of the automobile, enhance the impact resistance of the automobile, and has good formability, rigidity, collision energy absorbing ability, and weldability. A typical CMnSi-based TRIP steel contains 0.1 to 0.2% C, 1% to 2% Mn, and 1% to 2% Si, and is subjected to hot rolling deformation heat treatment or cold rolling + heat treatment. The structure of TRIP steel consists of 50% to 60% ferrite, 25% to 40% bainite or a small amount of martensite and 5% to 15% retained austenite. However, the surface of the TRIP steel is liable to form an oxide of Si, causing serious surface defects, so the wettability is poor, and there is a bottleneck of poor galvanizing adhesion property, and it is difficult to achieve the corrosion resistance of the hot-dip galvanized steel sheet.
从检索到的中国专利申请号为200810119818、名称为“一种高强度冷轧热镀锌用TRIP钢板及其制备方法”专利文献中可知,其基板化学组成(wt
%)为C:0.1~0.4、Si≤0.06、Mn:0.5~2.5、Al:0.5~2.0、P≤0.03、S≤0.02、Nb:0.01~0.10、Ti:0.01~0.10、Cu:0.1~1.0、Ni:0.1~0.6,余量为Fe,该文献介绍的钢板是采用Nb、Ti微合金化,另外还添加了Cu、Ni等强化元素。其存在的不足:其实施例中添加了0.54%的Cu元素,由于Cu含量过高,易造成镀锌钢板基材的热脆性,对塑性产生不利影响,为了改善加入Cu所带来的塑性的恶化,同时加了0.31%的Ni,仅这一含量的Ni就会使每吨钢板成本提高600元以上,而且其实施例中有高达0.24%的C以及添加的其它元素,对钢板的焊接不利。从其实施例中的性能来看,材料的延伸率很低,均不超过27.0%。The chemical composition of the substrate is known from the patent document No. 200810119818, entitled "A TRIP steel sheet for high-strength cold-rolled hot-dip galvanizing and its preparation method".
%) is C: 0.1 to 0.4, Si ≤ 0.06, Mn: 0.5 to 2.5, Al: 0.5 to 2.0, P ≤ 0.03, S ≤ 0.02, Nb: 0.01 to 0.10, Ti: 0.01 to 0.10, Cu: 0.1 to 1.0 Ni: 0.1~0.6, the balance is Fe. The steel plate introduced in this document is made of Nb and Ti microalloyed, and other strengthening elements such as Cu and Ni are added. The deficiency of its existence: 0.54% of Cu element is added in the embodiment. Due to the high Cu content, the hot brittleness of the galvanized steel sheet substrate is easily caused, which has an adverse effect on plasticity, in order to improve the plasticity caused by the addition of Cu. Deterioration, while adding 0.31% Ni, only this content of Ni will increase the cost per ton of steel plate by more than 600 yuan, and in its embodiment, up to 0.24% of C and other elements added, which is not good for the welding of steel plates. . From the properties in the examples, the elongation of the materials was very low, and both did not exceed 27.0%.
本发明的目的在于克服目前存在的拉延性能和镀锌性能较差等不足,提供一种通过改变化学成分和生产工艺,使镀锌钢板锌层附着性好,应***化指数即n值不低于0.23,屈服强度为400~450MPa,抗拉强度为不低于600MPa,延伸率不低于28%的热镀锌钢板及其生产方法。
The purpose of the invention is to overcome the shortcomings such as the drawing property and the poor galvanizing performance, and provide a zinc layer of the galvanized steel sheet with good adhesion by changing the chemical composition and the production process, and the strain hardening index is not low. A hot-dip galvanized steel sheet having a yield strength of 400 to 450 MPa, a tensile strength of not less than 600 MPa, and an elongation of not less than 28% at 0.23 and a production method thereof.
实现上述目的的技术措施:Technical measures to achieve the above objectives:
高应***化指数的热镀锌高强钢,其基板的组分及重量百分比为:C:0.11~0.20,Al:0.51~1.22,Mn:1.50~2.00,Si:0.07~0.30,Cr:1.0~2.0,P≤0.015,S≤0.015,余量为Fe和不可避免的杂质。High-strain hardening index of hot-dip galvanized high-strength steel, the composition and weight percentage of the substrate are: C: 0.11~0.20, Al: 0.51~1.22, Mn: 1.50~2.00, Si: 0.07~0.30, Cr: 1.0~2.0 , P ≤ 0.015, S ≤ 0.015, the balance is Fe and unavoidable impurities.
其在于:还添加重量百分比为:Nb:0.10~0.20,Mo:0.01~0.05,V:0.01~0.05中的一种或几种。The method further comprises: adding one or more of weight percentages: Nb: 0.10 to 0.20, Mo: 0.01 to 0.05, and V: 0.01 to 0.05.
生产高应***化指数的热镀锌高强钢的方法,其步骤:A method for producing a high strain hardening index of hot-dip galvanized high-strength steel, the steps of which:
1)在真空度为67~134Pa条件下进行冶炼,冶炼温度控制为1590~1630℃,并连铸成坯;1) Smelting under the condition of a vacuum degree of 67~134Pa, the smelting temperature is controlled to be 1590~1630 °C, and continuously cast into a billet;
2)将连铸坯加热到1200~1270℃,并在此温度下保温160~200分钟;2) heating the continuous casting billet to 1200~1270 °C, and maintaining at this temperature for 160~200 minutes;
3)进行粗轧,控制其粗轧温度为1080~1120℃;3) rough rolling, controlling the rough rolling temperature to be 1080~1120 ° C;
4)进行终轧,控制其终轧温度为860~900℃,板厚控制在3~3.5毫米;4) Perform final rolling, control the finishing temperature to 860~900 °C, and control the thickness of the plate to 3~3.5 mm;
5)进行卷取,控制其卷取温度为580~620℃;5) performing coiling and controlling the coiling temperature to be 580~620 °C;
6)进行冷轧,控制其总压下率为66~73%,板厚控制在0.8~1.2毫米;6) Perform cold rolling, control the total reduction rate of 66~73%, and control the thickness of the plate to 0.8~1.2 mm;
7)进行热镀锌:7) Perform hot dip galvanizing:
a、将经冷轧后的钢板加热到780~798℃; a, the cold rolled steel plate is heated to 780 ~ 798 ° C;
b、在温度为780~798℃的条件下保温50~80秒; b. Keep the temperature at 780~798 °C for 50~80 seconds;
c、进行快速冷却,在冷却速度为30~50℃/秒下使钢板冷却到480~510℃; c, rapid cooling, cooling the steel plate to 480 ~ 510 ° C at a cooling rate of 30 ~ 50 ° C / sec;
d、进行镀锌,在锌液温度为465~490℃下,浸镀5~9秒; d, galvanizing, immersion plating for 5 to 9 seconds at a temperature of 465 to 490 ° C;
e、进行再冷却,在冷却速度为5~17℃/秒下使钢板冷却到室温。 e. Perform re-cooling, and cool the steel sheet to room temperature at a cooling rate of 5 to 17 ° C / sec.
其特征在于:所述的锌液中含铝的重量百分比为0.20~0.24。It is characterized in that: the zinc liquid contains aluminum in a weight percentage of 0.20 to 0.24.
钢中各元素的作用及机理如下。The role and mechanism of each element in steel are as follows.
C:C是奥氏体稳定性元素,其价格低廉,同时,C也是间隙强化元素,强化效果十分明显,C含量越高对强化效果越好。但C含量过高,不利于保证材料的焊接性能。除了增加强度以外,C在本发明中对塑性的改善也起到至关重要的作用。高温下C可固溶在残余奥氏体中,提高残余奥氏体的稳定性,通过控制冷却,在室温下获得稳定性适中的残余奥氏体。残余奥氏体在外力作用下,发生组织转变,转变为马氏体,可以提高材料强度。因此,将C含量上限控制在0.20%以下,下限控制在0.11%以上。C: C is an austenite stability element, and its price is low. At the same time, C is also a gap strengthening element, and the strengthening effect is very obvious. The higher the C content, the better the strengthening effect. However, the C content is too high, which is not conducive to ensuring the welding performance of the material. In addition to increasing the strength, C plays a crucial role in the improvement of plasticity in the present invention. At high temperature, C can be dissolved in the retained austenite to improve the stability of the retained austenite. By controlling the cooling, a moderately stable retained austenite is obtained at room temperature. Residual austenite undergoes a structural transformation under external force and transforms into martensite, which can increase the strength of the material. Therefore, the upper limit of the C content is controlled to 0.20% or less, and the lower limit is controlled to be 0.11% or more.
Al:目前,常规高强钢大都通过添加Si元素来提高残余奥氏体的数量与稳定性,抑制渗碳体的形成,但Si元素容易在钢板表面形成致密的氧化层Mn2SiO4,从而影响材料的镀锌性能,所以本发明采用Al元素代替大部分Si元素。Al也和Si元素一样,具有细化晶粒和稳定残余奥氏体作用,抑制渗碳体的形成,Al属于非碳化物形成元素,促进碳原子从铁素体中扩散到奥氏体中,从而增加残余奥氏体的数量和稳定性。Al在工业生产连续浇铸过程中容易堵塞水口,因此,Al元素在钢中的上限含量控制在1.22%以下。Al: At present, conventional high-strength steel mostly increases the quantity and stability of retained austenite by adding Si element, and inhibits the formation of cementite. However, Si element easily forms a dense oxide layer Mn 2 SiO 4 on the surface of the steel sheet, thus affecting The galvanizing properties of the material, so the present invention uses Al instead of most of the Si. Al, like Si, has fine grain and stabilized retained austenite to inhibit the formation of cementite. Al is a non-carbide forming element that promotes the diffusion of carbon atoms from ferrite into austenite. Thereby increasing the amount and stability of retained austenite. Al is prone to block the nozzle during continuous casting in industrial production. Therefore, the upper limit of Al element in steel is controlled to be less than 1.22%.
Si:Si在本发明中起进一步细化晶粒和稳定残余奥氏体的作用,弥补Al含量不足导致的残余奥氏体数量和稳定性不足的缺憾,同时,Si元素也对钢板基体具有强化作用。但由于Si元素容易在钢板表面形成致密的氧化层Mn2SiO4,从而影响材料的镀锌性能,故限定在0.07~0.30%。In the present invention, Si:Si further refines grains and stabilizes retained austenite, and compensates for the lack of retained austenite and insufficient stability due to insufficient Al content. Meanwhile, Si element also strengthens the steel substrate. effect. However, since the Si element easily forms a dense oxide layer Mn 2 SiO 4 on the surface of the steel sheet, thereby affecting the galvanizing performance of the material, it is limited to 0.07 to 0.30%.
Mn:Mn元素是常规的强韧化元素,作为奥氏体形成元素,“不仅能扩大奥氏体区,降低终轧温度,推迟奥氏体转变,还可以同时起到细化晶粒和稳定残余奥氏体的作用。但Mn元素含量太高,一方面增加成本,另一方面增加钢的淬透性,使焊接组织出现硬化层导致裂纹焊缝及热影响区裂纹敏感性增高。因此,将Mn含量上限控制在2.0%以下,下限控制在1.50%以上。Mn: Mn element is a conventional strengthening and toughening element. As an austenite forming element, “not only can expand the austenite region, lower the finishing temperature, delay the transformation of austenite, but also refine grains and stabilize at the same time. The role of retained austenite. However, the content of Mn is too high, on the one hand, the cost is increased, on the other hand, the hardenability of the steel is increased, and the hardened layer of the welded structure causes the crack weld and the crack sensitivity of the heat-affected zone to be increased. The upper limit of the Mn content is controlled to 2.0% or less, and the lower limit is controlled to 1.50% or more.
Cr:Cr是铁素体形成元素,Cr元素能够显著提高钢的强度,弥补了本发明因用Al代替Si导致的强度降低的不利影响,同时,Cr元素又能提高钢的抗氧化性和耐腐蚀性。Cr含量太低,钢板的强度不足,太高增加钢板成本,也影响钢板的综合性能,因此Cr控制在1.0~2.0%范围内。Cr: Cr is a ferrite forming element, and Cr element can significantly increase the strength of steel, and compensates for the adverse effect of the strength reduction caused by Al instead of Si in the present invention, and at the same time, Cr element can improve the oxidation resistance and resistance of steel. Corrosive. The Cr content is too low, the strength of the steel sheet is insufficient, and the steel sheet costs are too high, which also affects the overall performance of the steel sheet, so the Cr is controlled within the range of 1.0 to 2.0%.
S:S对本发明材料的塑韧性不利,降低耐腐蚀性,所以越低越好。S:S is disadvantageous to the plastic toughness of the material of the present invention, and the corrosion resistance is lowered, so the lower the better.
P:P对本发明材料的塑性、焊接性和成形性不利,所以越低越好。P:P is detrimental to the plasticity, weldability and formability of the material of the present invention, so the lower the better.
Nb、Ti是一种强碳氮化物形成元素,有利于析出强化,并且可以阻止高温奥氏体过分长大,但Nb含量过高,容易导致碳氮化物偏聚,其加工性变差,同时,增加了材料成本。Nb and Ti are strong carbonitride forming elements, which are favorable for precipitation strengthening, and can prevent high temperature austenite from growing excessively, but the Nb content is too high, which tends to cause carbonitride segregation, and the processability thereof is deteriorated. , increased material costs.
Mo:Mo能使钢的晶粒细化,在高温时保持足够的强度和抗蠕变能力。Mo: Mo refines the grain of steel and maintains sufficient strength and creep resistance at high temperatures.
V:V能够抑制从退火温度快冷时珠光体或者渗碳体的形成,同时,V能提高强度和韧性,还可提高抗氢腐蚀能力。V:V can suppress the formation of pearlite or cementite when it is rapidly cooled from the annealing temperature. At the same time, V can improve strength and toughness, and can also improve hydrogen corrosion resistance.
本发明解决了传统高Si含量的高强钢存在的难以镀锌的问题,具有良好的可镀性、很高的拉延性能、良好的焊接性能、高的耐腐蚀性以及良好的成形性能,体现了具有良好的市场应用前景及显著的社会效益和经济效益。与传统镀锌板相比,采用本发明材料具有以下优点:The invention solves the problem that the traditional high Si content high strength steel has difficulty in galvanizing, has good platability, high drawing property, good welding performance, high corrosion resistance and good forming performance, and reflects It has a good market application prospect and significant social and economic benefits. Compared with conventional galvanized sheets, the use of the material of the invention has the following advantages:
(1)发明材料中含有7%以上的残余奥氏体,在成形过程中,残余奥氏体因吸收外部能量而转化为马氏体,这样,材料不仅表现出良好的延伸性能和拉延性能,同时,使材料强度进一步提高,由于弯曲变形应力的释放,变形后零件尺寸保持稳定。(1) The invention contains more than 7% of retained austenite. During the forming process, the retained austenite is transformed into martensite by absorbing external energy, so that the material not only exhibits good elongation and drawability. At the same time, the strength of the material is further improved, and the size of the part after deformation is kept stable due to the release of the bending deformation stress.
(2)发明材料含有稳定的残余奥氏体,在焊接过程中,残余奥氏体可以吸收裂纹尖端应力、缓解裂纹形成与扩展,因此,零件焊接过程中未发生裂纹及开裂,具有良好的焊接性能。(2) The invention material contains stable retained austenite. During the welding process, the retained austenite can absorb the crack tip stress and alleviate the crack formation and expansion. Therefore, no cracks and cracks occur during the welding of the parts, and the welding is good. performance.
(3)发明材料在保证基本力学性能的同时,最为优异的是通过本发明合理的化学成分和镀锌工艺,使其具有良好的镀锌性能,不但具有高强度和高拉延性,同时具有耐腐蚀性,是高端轿车选取的理想结构件用钢板。(3) The invention material is excellent in ensuring the basic mechanical properties, and is excellent in the galvanizing property by the reasonable chemical composition and galvanizing process of the invention, not only has high strength and high drawability, but also has resistance. Corrosive, it is the ideal structural steel plate for high-end cars.
实施例1:高应***化指数的热镀锌高强钢,其基板的组分及重量百分比为:C:0.15,Al:1.00,Mn:1.76,Si:0.15,Cr:1.50,P:0.012,S:0.010,Nb:0.10,余量为Fe和不可避免的杂质。Example 1: Hot-dip galvanized high-strength steel with high strain hardening index, the composition and weight percentage of the substrate were: C: 0.15, Al: 1.00, Mn: 1.76, Si: 0.15, Cr: 1.50, P: 0.012, S : 0.010, Nb: 0.10, the balance is Fe and unavoidable impurities.
生产高应***化指数的热镀锌高强钢的方法,其步骤:A method for producing a high strain hardening index of hot-dip galvanized high-strength steel, the steps of which:
1)在真空度为105Pa条件下进行冶炼,冶炼温度控制为1620~1630℃,并连铸成坯;1) smelting under the condition of a vacuum of 105 Pa, the smelting temperature is controlled to be 1620~1630 ° C, and continuously cast into a billet;
2)将连铸坯加热到1260~1270℃,并在此温度下保温178分钟;2) heating the continuous casting billet to 1260~1270 ° C, and maintaining at this temperature for 178 minutes;
3)进行粗轧,控制其粗轧温度为1110~1120℃;3) rough rolling, control the rough rolling temperature is 1110 ~ 1120 ° C;
4)进行终轧,控制其终轧温度为890~900℃,板厚控制在3.5毫米;4) Perform final rolling, control its finishing temperature to 890~900 °C, and control the thickness of the plate to 3.5 mm;
5)进行卷取,控制其卷取温度为610~620℃;5) performing coiling and controlling the coiling temperature to be 610~620 °C;
6)进行冷轧,控制其总压下率为66%,板厚控制在1.2毫米;6) cold rolling, control the total reduction rate of 66%, the thickness of the plate is controlled at 1.2 mm;
7)进行热镀锌:7) Perform hot dip galvanizing:
a、将经冷轧后的钢板加热到792~798℃,加热时间为220秒; a, the cold rolled steel plate is heated to 792 ~ 798 ° C, heating time is 220 seconds;
b、在温度为792~798℃的条件下保温80秒; b, holding at a temperature of 792 ~ 798 ° C for 80 seconds;
c、进行快速冷却,在冷却速度为40~45℃/秒下使钢板冷却到500~510℃; c, rapid cooling, cooling the steel plate to 500 ~ 510 ° C at a cooling rate of 40 ~ 45 ° C / sec;
d、进行镀锌,在锌液温度为480~490℃下浸镀9秒,其锌液中含铝的重量百分比为0.20; d, galvanizing, immersion plating at a temperature of 480 ~ 490 ° C for 9 seconds, the weight percentage of aluminum in the zinc solution is 0.20;
e、进行再冷却,在冷却速度为17℃/秒下使钢板冷却到室温。 e. Perform re-cooling, and cool the steel sheet to room temperature at a cooling rate of 17 ° C / sec.
实施例2:高应***化指数的热镀锌高强钢,其基板的组分及重量百分比为:C:0.15,Al:1.10,Mn:1.75,Si:0.21,Cr:1.26,P:0.015,S:0.009,余量为Fe和不可避免的杂质。Example 2: Hot-dip galvanized high-strength steel with high strain hardening index, the composition and weight percentage of the substrate were: C: 0.15, Al: 1.10, Mn: 1.75, Si: 0.21, Cr: 1.26, P: 0.015, S : 0.009, the balance is Fe and unavoidable impurities.
生产高应***化指数的热镀锌高强钢的方法,其步骤:A method for producing a high strain hardening index of hot-dip galvanized high-strength steel, the steps of which:
1)在真空度为67Pa条件下进行冶炼,冶炼温度控制为1600~1610℃,并连铸成坯;1) Smelting is carried out under the condition of a vacuum degree of 67 Pa, and the smelting temperature is controlled to be 1600 to 1610 ° C, and continuously cast into a billet;
2)将连铸坯加热到1220~1235℃,并在此温度下保温170分钟;2) heating the continuous casting billet to 1220~1235 ° C, and holding at this temperature for 170 minutes;
3)进行粗轧,控制其粗轧温度为1090~1105℃;3) rough rolling, control the rough rolling temperature is 1090 ~ 1105 ° C;
4)进行终轧,控制其终轧温度为880~890℃,板厚控制在3.2毫米;4) Perform final rolling, control the finishing temperature to 880~890 °C, and control the thickness of the plate to 3.2 mm;
5)进行卷取,控制其卷取温度为590~595℃;5) performing coiling and controlling the coiling temperature to be 590~595 °C;
6)进行冷轧,控制其总压下率为69%,板厚控制在1.0毫米;6) Perform cold rolling, control the total reduction rate to be 69%, and control the thickness of the plate to 1.0 mm;
7)进行热镀锌:7) Perform hot dip galvanizing:
a、将经冷轧后的钢板加热到785~795℃,加热时间为210秒; a, the cold rolled steel plate is heated to 785 ~ 795 ° C, the heating time is 210 seconds;
b、在温度为785~795℃的条件下保温60秒; b, holding at a temperature of 785 ~ 795 ° C for 60 seconds;
c、进行快速冷却,在冷却速度为35~40℃/秒下使钢板冷却到485~495℃; c, rapid cooling, cooling the steel plate to 485 ~ 495 ° C at a cooling rate of 35 ~ 40 ° C / sec;
d、进行镀锌,在锌液温度为465~475℃下使浸泡6秒,其锌液中含铝的重量百分比为0.24; d, galvanizing, soaking for 6 seconds at a temperature of 465 to 475 ° C of zinc liquid, the weight percentage of aluminum in the zinc liquid is 0.24;
e、进行再冷却,在冷却速度为10℃/秒下使钢板冷却到室温。 e. Perform re-cooling, and cool the steel sheet to room temperature at a cooling rate of 10 ° C / sec.
实施例3:高应***化指数的热镀锌高强钢,其基板的组分及重量百分比为:C:0.11,Al:1.22,Mn:1.55,Si:0.07,Cr:1.0,P:0.013,S:0.008,余量为Fe和不可避免的杂质。Example 3: Hot-dip galvanized high-strength steel with high strain hardening index, the composition and weight percentage of the substrate were: C: 0.11, Al: 1.22, Mn: 1.55, Si: 0.07, Cr: 1.0, P: 0.013, S : 0.008, the balance is Fe and unavoidable impurities.
生产高应***化指数的热镀锌高强钢的方法,其步骤:A method for producing a high strain hardening index of hot-dip galvanized high-strength steel, the steps of which:
1)在真空度为80Pa条件下进行冶炼,冶炼温度控制为1590~1595℃,并连铸成坯;1) Smelting is carried out under the condition of a vacuum degree of 80 Pa, and the smelting temperature is controlled to be 1590 to 1595 ° C, and continuously cast into a billet;
2)将连铸坯加热到1200~1210℃,并在此温度下保温160分钟;2) heating the continuous casting billet to 1200~1210 ° C, and maintaining at this temperature for 160 minutes;
3)进行粗轧,控制其粗轧温度为1080~1096℃;3) rough rolling, controlling the rough rolling temperature to be 1080~1096 ° C;
4)进行终轧,控制其终轧温度为860~875℃,板厚控制在3毫米;4) Perform final rolling, control its finishing temperature to 860~875 °C, and control the thickness of the plate to 3 mm;
5)进行卷取,控制其卷取温度为580~595℃;5) performing coiling and controlling the coiling temperature to be 580~595 °C;
6)进行冷轧,控制其总压下率为73%,板厚控制在0.8毫米;6) cold rolling, control the total reduction rate of 73%, the thickness of the plate is controlled at 0.8 mm;
7)进行热镀锌:7) Perform hot dip galvanizing:
a、将经冷轧后的钢板加热到780~785℃,加热时间为200秒; a, the cold rolled steel plate is heated to 780 ~ 785 ° C, heating time is 200 seconds;
b、在温度为780~785℃的条件下保温50秒; b, holding at a temperature of 780 ~ 785 ° C for 50 seconds;
c、进行快速冷却,在冷却速度为30~35℃/秒下使钢板冷却到480~490℃; c, rapid cooling, cooling the steel plate to 480 ~ 490 ° C at a cooling rate of 30 ~ 35 ° C / sec;
d、进行镀锌,在锌液温度为465~475℃下浸镀5秒,其锌液中含铝的重量百分比为0.22; d, galvanizing, immersion plating for 5 seconds at a temperature of 465 to 475 ° C, the weight percentage of aluminum in the zinc solution is 0.22;
e、进行再冷却,在冷却速度为5℃/秒下使钢板冷却到室温。 e. Perform re-cooling, and cool the steel sheet to room temperature at a cooling rate of 5 ° C / sec.
实施例4:高应***化指数的热镀锌高强钢,其基板的组分及重量百分比为:C:0.20,Al:0.50,Mn:2.0,Si:0.
30,Cr:1.20,P:0.009,S:0.008,Mo:0.01,余量为Fe和不可避免的杂质。Example 4: Hot-dip galvanized high-strength steel with high strain hardening index, the composition and weight percentage of the substrate are: C: 0.20, Al: 0.50, Mn: 2.0, Si: 0.
30, Cr: 1.20, P: 0.009, S: 0.008, Mo: 0.01, the balance being Fe and unavoidable impurities.
生产高应***化指数的热镀锌高强钢的方法,其步骤:A method for producing a high strain hardening index of hot-dip galvanized high-strength steel, the steps of which:
1)在真空度为134Pa条件下进行冶炼,冶炼温度控制为1600~1610℃,并连铸成坯;1) Smelting is carried out under the condition of a vacuum degree of 134 Pa, and the smelting temperature is controlled to be 1600 to 1610 ° C, and continuously cast into a billet;
2)将连铸坯加热到1200~1215℃,并在此温度下保温200分钟;2) heating the continuous casting billet to 1200~1215 °C, and keeping it at this temperature for 200 minutes;
3)进行粗轧,控制其粗轧温度为1090~1100℃;3) rough rolling, control the rough rolling temperature is 1090 ~ 1100 ° C;
4)进行终轧,控制其终轧温度为875~885℃,板厚控制在3.2毫米;4) Perform final rolling, control the finishing temperature to 875~885 °C, and control the thickness of the plate to 3.2 mm;
5)进行卷取,控制其卷取温度为585~595℃;5) performing coiling and controlling the coiling temperature to be 585~595 °C;
6)进行冷轧,控制其总压下率为69%,板厚控制在1.0毫米;6) Perform cold rolling, control the total reduction rate to be 69%, and control the thickness of the plate to 1.0 mm;
7)进行热镀锌:7) Perform hot dip galvanizing:
a、将经冷轧后的钢板加热到785~790℃,加热时间为220秒; a, the cold rolled steel plate is heated to 785 ~ 790 ° C, heating time is 220 seconds;
b、在温度为785~790℃的条件下保温70秒; b, holding at a temperature of 785 ~ 790 ° C for 70 seconds;
c、进行快速冷却,在冷却速度为45~50℃/秒下使钢板冷却到485~495℃; c, rapid cooling, cooling the steel plate to 485 ~ 495 ° C at a cooling rate of 45 ~ 50 ° C / sec;
d、进行镀锌,在锌液温度为465~475℃下浸镀9秒,其锌液中含铝的重量百分比为0.22; d, galvanizing, immersion plating for 9 seconds at a temperature of 465 to 475 ° C, the weight percentage of aluminum in the zinc solution is 0.22;
e、进行再冷却,在冷却速度为15℃/秒下使钢板冷却到室温。 e. Perform re-cooling, and cool the steel sheet to room temperature at a cooling rate of 15 ° C / sec.
实施例5:高应***化指数的热镀锌高强钢,其基板的组分及重量百分比为:C:0.16,Al:0.94,Mn:1.52,Si:0.22,Cr:2.0,P:0.011,S:0.010,Mo:0.05,V:0.01,余量为Fe和不可避免的杂质。Example 5: Hot-dip galvanized high-strength steel with high strain hardening index, the composition and weight percentage of the substrate were: C: 0.16, Al: 0.94, Mn: 1.52, Si: 0.22, Cr: 2.0, P: 0.011, S : 0.010, Mo: 0.05, V: 0.01, the balance being Fe and unavoidable impurities.
生产高应***化指数的热镀锌高强钢的方法,其步骤:A method for producing a high strain hardening index of hot-dip galvanized high-strength steel, the steps of which:
1)在真空度为80Pa条件下进行冶炼,冶炼温度控制为1620~1630℃,并连铸成坯;1) Smelting is carried out under the condition of a vacuum degree of 80 Pa, and the smelting temperature is controlled to be 1620 to 1630 ° C, and continuously cast into a billet;
2)将连铸坯加热到1230~1245℃,并在此温度下保温160分钟;2) heating the continuous casting billet to 1230~1245 ° C, and maintaining at this temperature for 160 minutes;
3)进行粗轧,控制其粗轧温度为1110~1120℃;3) rough rolling, control the rough rolling temperature is 1110 ~ 1120 ° C;
4)进行终轧,控制其终轧温度为885~895℃,板厚控制在3.2毫米;4) Perform final rolling, control the finishing temperature to 885~895 °C, and control the thickness of the plate to 3.2 mm;
5)进行卷取,控制其卷取温度为595~605℃;5) performing coiling and controlling the coiling temperature to be 595~605 °C;
6)进行冷轧,控制其总压下率为69%,板厚控制在1.0毫米;6) Perform cold rolling, control the total reduction rate to be 69%, and control the thickness of the plate to 1.0 mm;
7)进行热镀锌:7) Perform hot dip galvanizing:
a、将经冷轧后的钢板加热到792~798℃,加热时间为200秒; a, the cold rolled steel plate is heated to 792 ~ 798 ° C, heating time is 200 seconds;
b、在温度为792~798℃的条件下保温50秒; b, holding at a temperature of 792 ~ 798 ° C for 50 seconds;
c、进行快速冷却,在冷却速度为45~49℃/秒下使钢板冷却到485~495℃; c, rapid cooling, cooling the steel plate to 485 ~ 495 ° C at a cooling rate of 45 ~ 49 ° C / sec;
d、进行镀锌,在锌液温度为465~475℃下浸镀8秒,其锌液中含铝的重量百分比为0.22; d, galvanizing, immersion plating for 8 seconds at a temperature of 465 to 475 ° C, the weight percentage of aluminum in the zinc solution is 0.22;
e、进行再冷却,在冷却速度为12℃/秒下使钢板冷却到室温。 e. Perform re-cooling, and cool the steel sheet to room temperature at a cooling rate of 12 ° C / sec.
实施例6:高应***化指数的热镀锌高强钢,其基板的组分及重量百分比为:C:0.15,Al:1.05,Mn:1.55,Si:0.18,Cr:1.10,P:0.008,S:0.006,Mo:0.01,V:0.05、Nb:0.20,余量为Fe和不可避免的杂质。Example 6: Hot-dip galvanized high-strength steel with high strain hardening index, the composition and weight percentage of the substrate were: C: 0.15, Al: 1.05, Mn: 1.55, Si: 0.18, Cr: 1.10, P: 0.008, S : 0.006, Mo: 0.01, V: 0.05, Nb: 0.20, the balance being Fe and unavoidable impurities.
生产高应***化指数的热镀锌高强钢的方法,其步骤:A method for producing a high strain hardening index of hot-dip galvanized high-strength steel, the steps of which:
1)在真空度为85Pa条件下进行冶炼,冶炼温度控制为1620~1628℃,并连铸成坯;1) Smelting under the condition of a vacuum of 85 Pa, the smelting temperature is controlled to be 1620~1628 ° C, and continuously cast into a billet;
2)将连铸坯加热到1235~1245℃,并在此温度下保温200分钟;2) heating the continuous casting billet to 1235~1245 ° C, and keeping it at this temperature for 200 minutes;
3)进行粗轧,控制其粗轧温度为1105~1115℃;3) performing rough rolling and controlling the rough rolling temperature to be 1105~1115 °C;
4)进行终轧,控制其终轧温度为880~890℃,板厚控制在3.0毫米;4) Perform final rolling, control the finishing temperature to 880~890 °C, and control the thickness of the plate to 3.0 mm;
5)进行卷取,控制其卷取温度为600~610℃;5) performing coiling and controlling the coiling temperature to be 600~610 °C;
6)进行冷轧,控制其总压下率为67%,板厚控制在1.0毫米;6) cold rolling, control the total reduction rate of 67%, the thickness of the plate is controlled at 1.0 mm;
7)进行热镀锌:7) Perform hot dip galvanizing:
a、将经冷轧后的钢板加热到780~790℃,加热时间为210秒; a, the cold rolled steel plate is heated to 780 ~ 790 ° C, the heating time is 210 seconds;
b、在温度为780~790℃的条件下保温60秒; b, holding at a temperature of 780 ~ 790 ° C for 60 seconds;
c、进行快速冷却,在冷却速度为40~45℃/秒下使钢板冷却到485~495℃; c, rapid cooling, cooling the steel plate to 485 ~ 495 ° C at a cooling rate of 40 ~ 45 ° C / sec;
d、进行镀锌,在锌液温度为465~475℃下浸镀7秒,其锌液中含铝的重量百分比为0.22; d, galvanizing, immersion plating for 7 seconds at a temperature of 465 to 475 ° C, the weight percentage of aluminum in the zinc solution is 0.22;
e、进行再冷却,在冷却速度为5℃/秒下使钢板冷却到室温。 e. Perform re-cooling, and cool the steel sheet to room temperature at a cooling rate of 5 ° C / sec.
上述实施例经检测,其性能检测结果见表1。 The above examples were tested, and the performance test results are shown in Table 1.
从表1中可看出,本发明的产品力学性能优于传统CMnSi系的TRIP钢,并且锌层附着性能优良,完全能满足汽车结构件生产的要求。It can be seen from Table 1 that the mechanical properties of the product of the present invention are superior to those of the conventional CMnSi-based TRIP steel, and the adhesion property of the zinc layer is excellent, and can fully meet the requirements for the production of automobile structural parts.
Claims (4)
1、高应***化指数的热镀锌高强钢,其基板的组分及重量百分比为:C:0.11~0.20,Al:0.51~1.22,Mn:1.50~2.00,Si:0.07~0.30,Cr:1.0~2.0,P≤0.015,S≤0.015,余量为Fe和不可避免的杂质。
1. High-strain hardening index of hot-dip galvanized high-strength steel, the composition and weight percentage of the substrate are: C: 0.11~0.20, Al: 0.51~1.22, Mn: 1.50~2.00, Si: 0.07~0.30, Cr: 1.0 ~2.0, P ≤ 0.015, S ≤ 0.015, the balance is Fe and unavoidable impurities.
2、如权利要求1所述的高应***化指数的热镀锌高强钢,其特征在于:还添加有重量百分比为:Nb:0.10~0.20,Mo:0.01~0.05,V:0.01~0.05中的一种或几种。2. The high-strain hardening index hot-dip galvanized high-strength steel according to claim 1, wherein the weight percentage is: Nb: 0.10 to 0.20, Mo: 0.01 to 0.05, and V: 0.01 to 0.05. One or several.
3、生产如权利要求1所述的高应***化指数的热镀锌高强钢的方法,其步骤:3. A method of producing a high strain hardening index hot dip galvanized high strength steel according to claim 1, the steps of:
1)在真空度为67~134Pa条件下进行冶炼,冶炼温度控制为1590~1630℃,并连铸成坯;1) Smelting under the condition of a vacuum degree of 67~134Pa, the smelting temperature is controlled to be 1590~1630 °C, and continuously cast into a billet;
2)将连铸坯加热到1200~1270℃,并在此温度下保温160~200分钟;2) heating the continuous casting billet to 1200~1270 °C, and maintaining at this temperature for 160~200 minutes;
3)进行粗轧,控制其粗轧温度为1080~1120℃;3) rough rolling, controlling the rough rolling temperature to be 1080~1120 ° C;
4)进行终轧,控制其终轧温度为860~900℃,板厚控制在3~3.5毫米;4) Perform final rolling, control the finishing temperature to 860~900 °C, and control the thickness of the plate to 3~3.5 mm;
5)进行卷取,控制其卷取温度为580~620℃;5) performing coiling and controlling the coiling temperature to be 580~620 °C;
6)进行冷轧,控制其总压下率为66~73%,板厚控制在0.8~1.2毫米;6) Perform cold rolling, control the total reduction rate of 66~73%, and control the thickness of the plate to 0.8~1.2 mm;
7)进行热镀锌:7) Perform hot dip galvanizing:
a、将经冷轧后的钢板加热到780~798℃; a, the cold rolled steel plate is heated to 780 ~ 798 ° C;
b、在温度为780~798℃的条件下保温50~80秒; b. Keep the temperature at 780~798 °C for 50~80 seconds;
c、进行快速冷却,在冷却速度为30~50℃/秒下使钢板冷却到480~510℃; c, rapid cooling, cooling the steel plate to 480 ~ 510 ° C at a cooling rate of 30 ~ 50 ° C / sec;
d、进行镀锌,在锌液温度为465~490℃下,浸镀5~9秒; d, galvanizing, immersion plating for 5 to 9 seconds at a temperature of 465 to 490 ° C;
e、进行再冷却,在冷却速度为5~17℃/秒下使钢板冷却到室温。 e. Perform re-cooling, and cool the steel sheet to room temperature at a cooling rate of 5 to 17 ° C / sec.
4、如权利要求3所述的生产高应***化指数的热镀锌高强钢的方法,其特征在于:所述的锌液中含铝的重量百分比为0.20~0.24。4. The method of producing high-strain hardening index hot-dip galvanized high-strength steel according to claim 3, wherein the zinc liquid has a weight percentage of aluminum of 0.20 to 0.24.
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WO2016005061A1 (en) * | 2014-07-07 | 2016-01-14 | Tata Steel Ijmuiden B.V. | Steel strip having high strength and high formability, the steel strip having a hot dip zinc based coating |
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CN101899619A (en) | 2010-12-01 |
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