WO2012022184A1 - Acier galvanisé à chaud à haute résistance doté d'un indice de durcissement par contrainte élevé et procédé de production de celui-ci - Google Patents

Acier galvanisé à chaud à haute résistance doté d'un indice de durcissement par contrainte élevé et procédé de production de celui-ci Download PDF

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Publication number
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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Prior art keywords
temperature
hot
dip galvanized
strength steel
cooling
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PCT/CN2011/075236
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English (en)
Chinese (zh)
Inventor
王立辉
陈宇
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武汉钢铁(集团)公司
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Publication of WO2012022184A1 publication Critical patent/WO2012022184A1/fr

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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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  • Engineering & Computer Science (AREA)
  • Organic Chemistry (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
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  • Chemical Kinetics & Catalysis (AREA)
  • Physics & Mathematics (AREA)
  • Oil, Petroleum & Natural Gas (AREA)
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  • Heat Treatment Of Sheet Steel (AREA)
  • Coating With Molten Metal (AREA)

Abstract

L'invention concerne un acier galvanisé à chaud à haute résistance constitué de (en % en poids) : C : 0,11 à 0,20, Al : 0,51 à 1,22, Mn : 1,50 à 2,00, Si : 0,07 à 0,30, Cr : 1,0 à 2,0 : P ≤ 0,015, S ≤ 0,015, et le solde constitué de fer et d'impuretés inévitables. Un procédé de production de celui-ci comprend les étapes suivantes : fusion et coulée continue en billette ; chauffage de la billette de coulée continue et préservation de la chaleur ; laminage grossier ; laminage final ; enroulement ; laminage à froid ; et galvanisation à chaud, c'est-à-dire chauffage de la plaque d'acier laminée à froid, préservation de la chaleur, refroidissement rapide à une température de 480 à 510 °C, galvanisation par trempage pendant 5 à 9 secondes, puis refroidissement à la température ambiante. L'acier galvanisé à chaud à haute résistance possède les caractéristiques d'une bonne aptitude à la galvanisation, d'une résistance élevée à la traction et de bonnes performances de soudage, d'une bonne résistance à la corrosion et d'une bonne aptitude au formage.
PCT/CN2011/075236 2010-08-14 2011-06-03 Acier galvanisé à chaud à haute résistance doté d'un indice de durcissement par contrainte élevé et procédé de production de celui-ci WO2012022184A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN201010253367.6 2010-08-14
CN2010102533676A CN101899619B (zh) 2010-08-14 2010-08-14 高应变硬化指数的热镀锌高强钢及其生产方法

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WO2016005061A1 (fr) * 2014-07-07 2016-01-14 Tata Steel Ijmuiden B.V. Bande d'acier douée d'une résistance élevée et d'une aptitude élevée au formage, portant un revêtement à base de zinc obtenu par immersion à chaud
CN113403550A (zh) * 2021-05-21 2021-09-17 鞍钢股份有限公司 高塑性耐疲劳的冷轧热镀锌dh1180钢板及制备方法
CN113462975A (zh) * 2021-06-29 2021-10-01 莱芜钢铁集团银山型钢有限公司 一种690MPa级高强钢及其制造方法
CN113546978A (zh) * 2021-06-21 2021-10-26 首钢集团有限公司 一种防护车辆用复杂形状构件的制备方法
CN114032475A (zh) * 2021-10-15 2022-02-11 首钢集团有限公司 一种高强度冷轧热镀锌中锰钢及其制备方法与热成形零部件
CN115181885A (zh) * 2021-04-02 2022-10-14 宝山钢铁股份有限公司 590MPa级别高成形性热镀铝锌或热镀锌铝镁双相钢及快速热处理制造方法
CN115323275A (zh) * 2022-09-05 2022-11-11 东北大学 一种高强高韧的稀土温轧低碳低锰trip钢及其制备方法
CN115612816A (zh) * 2022-09-30 2023-01-17 攀钢集团攀枝花钢铁研究院有限公司 含硼钢制备复相钢、热成形用钢镀层板的方法
CN116254487A (zh) * 2023-02-01 2023-06-13 攀枝花学院 一种含钒热镀锌钢板及其热轧方法

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CN101899619B (zh) * 2010-08-14 2012-04-25 武汉钢铁(集团)公司 高应变硬化指数的热镀锌高强钢及其生产方法
CN102154604A (zh) * 2011-03-23 2011-08-17 武汉钢铁(集团)公司 一种相变诱导塑性热镀锌钢板的制备工艺
CN102719751B (zh) * 2011-03-29 2015-03-11 鞍钢股份有限公司 一种高强度冷轧热镀锌双相钢板及其制造方法
CN106435396B (zh) * 2016-09-09 2018-06-08 武汉钢铁有限公司 一种耐高温抗硫化氢腐蚀的压力容器用钢板及其制造方法

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CN115181885A (zh) * 2021-04-02 2022-10-14 宝山钢铁股份有限公司 590MPa级别高成形性热镀铝锌或热镀锌铝镁双相钢及快速热处理制造方法
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CN115612816B (zh) * 2022-09-30 2024-02-02 攀钢集团攀枝花钢铁研究院有限公司 含硼钢制备复相钢、热成形用钢镀层板的方法
CN116254487A (zh) * 2023-02-01 2023-06-13 攀枝花学院 一种含钒热镀锌钢板及其热轧方法
CN116254487B (zh) * 2023-02-01 2024-05-17 攀枝花学院 一种含钒热镀锌钢板及其热轧方法

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