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CN118256819A - A galvanized enhanced formability dual-phase steel and its production method - Google Patents

A galvanized enhanced formability dual-phase steel and its production method Download PDF

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Publication number
CN118256819A
CN118256819A CN202410695724.6A CN202410695724A CN118256819A CN 118256819 A CN118256819 A CN 118256819A CN 202410695724 A CN202410695724 A CN 202410695724A CN 118256819 A CN118256819 A CN 118256819A
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China
Prior art keywords
dual
phase steel
galvanized
heating
enhanced
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Pending
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CN202410695724.6A
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Chinese (zh)
Inventor
王朝
李杨
邝霜
田秀刚
王淑华
杨峰
于延钢
池永清
张靖雨
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Tangshan Iron and Steel Group Co Ltd
HBIS Co Ltd Tangshan Branch
Hegang Leting Steel Co Ltd
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Tangshan Iron and Steel Group Co Ltd
HBIS Co Ltd Tangshan Branch
Hegang Leting Steel Co Ltd
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Publication of CN118256819A publication Critical patent/CN118256819A/en
Pending legal-status Critical Current

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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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • 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
    • C21D2211/001—Austenite
    • 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
    • C21D2211/008—Martensite

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

The invention discloses galvanized enhanced formability dual-phase steel and a production method thereof, wherein the chemical components of the dual-phase steel comprise ：C：0.17～0.25%,Mn：1.50～2.70%,S≤0.005%,P≤0.020%,Si：0.20～1.00%,Als：0.20～1.20%,Nb：0.02～0.080%,Cr:0.20～1.00%, mass percent of Fe and non-removable impurities; the production method comprises continuous casting, heating, hot rolling, cold rolling, continuous annealing, hot galvanizing and finishing procedures. The dual-phase steel provided by the invention has a structure of ferrite, martensite and residual austenite, and the yield strength is Rp 0.2: 550-750 MPa, tensile strength is more than or equal to 980MPa, elongation after fracture A 80 is more than or equal to 15%, and cold forming performance is good.

Description

Galvanized enhanced formability dual-phase steel and production method thereof
Technical Field
The invention belongs to the technical field of metallurgy, and particularly relates to galvanized enhanced formability dual-phase steel and a production method thereof.
Background
Along with the high-speed development of the automobile industry, the application of the high-strength steel becomes the development direction of various large-vehicle enterprises, wherein the cold-rolled high-strength dual-phase steel (DP steel) is the most widely applied steel type at present. With the increasing complexity of automobile structural design, the requirement on the extensibility of materials is higher and higher, and the application of traditional DP steel is limited in the face of complex drawing forming parts. As the DH steel of the upgrade edition of the traditional DP steel, a small amount of residual austenite is introduced on the basis of ferrite and martensite dual phases, the TRIP effect of the residual austenite transformation induced plasticity is utilized, and the transformation strengthening and plasticity growth mechanism is introduced to improve the strength and toughness of the material. In view of the above, the invention provides a galvanized enhanced formability dual-phase steel and a production method thereof through component design and process control, which meet the requirements of corresponding products with plating layers.
Disclosure of Invention
The invention aims to solve the technical problem of providing galvanized enhanced formability dual-phase steel and also provides a production method of the galvanized enhanced formability dual-phase steel.
In order to solve the technical problems, the invention adopts the following technical scheme:
the galvanized double-phase steel with enhanced formability comprises the chemical components of ：C：0.17～0.25%,Mn：1.50～2.70%,S≤0.005%,P≤0.020%,Si：0.20～1.00%,Als：0.20～1.20%,Nb：0.02～0.080%,Cr:0.20～1.00%, mass percent of Fe and non-removable impurities.
Further, the galvanized enhanced formability dual-phase steel comprises the chemical components of ：C：0.19～0.23%,Mn：2.00～2.40%,S≤0.003%,P≤0.015%,Si：0.50～0.80%,Als：0.60～1.00%,Nb：0.020～0.050%,Cr：0.20～0.60%, by mass percent and the balance of Fe and non-removable impurities.
The steel plate disclosed by the invention has the following chemical components:
C: in the invention, carbon atoms are taken as basic elements in DH steel, are solid-dissolved at lattice defects of austenite and martensite matrix in a gap diffusion mode, play roles of expanding and stabilizing austenite and strengthening deformation resistance of matrix, and are main elements for improving bake hardening characteristic values, but hard phase structures are not easily obtained due to too low carbon content (less than or equal to 0.08%), the strength is ensured due to the fact that the ultra-high strength is not more than 1000MPa, the strength is ensured due to the fact that a large amount of Mn, cr and other alloy elements are required to be added, the shaping and toughness of the steel are weakened due to the fact that the carbon content is too high (more than or equal to 0.35%), and meanwhile, the welding performance is deteriorated, and therefore the carbon content is designed to be 0.17-0.25%, and preferably 0.19-0.23%.
Mn: manganese is one of main elements for stabilizing austenite in DH steel, the hardenability of the steel is obviously improved, pearlite transformation is delayed by reducing the Ms temperature, and the critical cooling speed of martensite formation is reduced, so that the cooling speed of a quick cooling section in the annealing process is effectively reduced, and further, a martensitic structure is facilitated to be obtained, meanwhile, manganese and carbon can both cause lattice distortion, a strengthening matrix is strengthened, the difference is that the radius of manganese is close to that of iron, the strengthening effect is smaller, the adverse effect of manganese on the plasticity and the welding performance of the steel is also smaller, and the manganese content is designed to be 1.50-2.70%, preferably 2.00-2.40% by combining with 980MPa grade Q & P steel production experience.
Si: si and Al are ferrite stabilizing elements. Silicon accelerates the segregation of carbon into austenite, has the functions of 'cleaning' and 'purifying' solid solution carbon in ferrite, reduces gap solid solution strengthening, and can inhibit the generation of coarse carbide during cooling. In a continuous ferrite matrix, the martensite can be promoted to be distributed in a fine microscopic form, and the double-phase steel is ensured to obtain good strengthening effect and good matching of strength and plasticity. In addition, silicon dissolved in ferrite can cause high strain hardening rate of residual austenite by inhibiting the cross sliding movement, so that the comprehensive mechanical property of the steel is improved, but the silicon content cannot be too high so as not to form composite oxide with low melting point, and the surface quality of the steel is affected, so that the silicon content is designed to be 0.20-1.00%, preferably 0.50-0.80%.
Al: aluminum is a strongly deoxidizing element, and in order to ensure that the oxygen content in the steel is as low as possible, a certain amount of aluminum needs to be added, and at the same time, soluble aluminum is often used as a microalloying element to combine nitrogen in the steel, and the very fine-dispersed AlN prevents the growth of austenite grains. During the gamma-alpha transformation, alN nucleates, thereby accelerating the austenitic transformation. The main role of AlN is to refine grains and to obtain aging resistance. When the Als content is too low, the effect thereof cannot be exerted; however, adding a large amount of aluminum tends to form alumina agglomerates. The aluminum content is therefore designed to be 0.20 to 1.20%, preferably 0.60 to 1.00%.
Nb: niobium can significantly raise the recrystallization temperature of steel and achieve grain refinement. The strain-induced precipitation of niobium carbide during hot rolling can prevent recovery and recrystallization of deformed austenite, and the deformed austenite structure after controlled rolling and controlled cooling can obtain a fine phase-change product. Meanwhile, in the annealing process, the fine niobium carbonitride precipitation can play a role in precipitation strengthening and is also an essential element for bake hardening characteristics, so that the niobium content is designed to be 0.02-0.08%, and preferably 0.02-0.05%.
Cr: a part of chromium dissolves into ferrite to form solid solution strengthening, thereby improving strength and hardness of ferrite. At the same time, the decomposition rate of austenite is slowed down, so that the chromium content is designed to be 0.20-1.00%, preferably 0.20-0.60%.
P: phosphorus is a harmful element in steel, and the lower the content is, the better. In view of cost, the content of the P element is controlled to be less than or equal to 0.020 percent, preferably less than or equal to 0.015 percent.
S: elemental sulfur is a harmful element in steel, and the lower the content, the better. In view of cost, the content of S element is controlled to be less than or equal to 0.005% and preferably less than or equal to 0.003% in the invention.
The thickness of the dual-phase steel is 1.0-2.2 mm.
The tensile strength of the dual-phase steel is more than or equal to 980MPa, and the yield strength Rp 0.2: 550-750 MPa and the elongation after break A 80 is more than or equal to 15 percent.
The dual-phase steel structure consists of ferrite, martensite and retained austenite.
The invention also provides a production method of the galvanized enhanced formability dual-phase steel, which comprises continuous casting, heating, hot rolling, cold rolling, continuous annealing and hot galvanizing, and finishing procedures;
Further, the continuous annealing and hot galvanizing process comprises the steps of heating a cold rolled sheet to 800-840 ℃, preserving heat for 60-120 s, slowly cooling to 650-700 ℃, slowly cooling to a cooling rate of 10-20 ℃/s, rapidly cooling to 300-370 ℃, rapidly cooling to 40-70 ℃/s, subsequently heating to 450-470 ℃, heating to 60-100 ℃/s, preserving heat for 15-30s, then entering a zinc pot, wherein the temperature of the zinc pot is 440-460 ℃, the time of the zinc pot is 5-8 s, and the final cooling temperature is 80-150 ℃.
Further, in the continuous casting process, the tundish temperature is 1510-1530 ℃, and the pulling speed is 1.2-1.4 m/min.
Further, the heating temperature of the heating process is 1200-1350 ℃ and the total heating time is 150-240 min.
Further, in the hot rolling process, the finish rolling temperature is 870-900 ℃ and the coiling temperature is 640-680 ℃.
Further, in the cold rolling process, the cold rolling reduction rate is more than or equal to 45 percent.
Further, in the finishing process, the finishing rolling force is 2000-5000KN.
The technical scheme of the invention has the beneficial effects that:
According to the invention, through reasonable component design and adopting the thought of Nb microalloying, grains are effectively refined, the austenite stability is improved, noble metals such as Mo and the like are not required to be added, and the alloy cost is low.
Compared with the traditional dual-phase steel, the galvanized DH980 provided by the invention introduces a certain amount of residual austenite, and realizes the characteristics of high strength and high plasticity under the TRIP effect.
The dual-phase steel provided by the invention has good mechanical properties, the tensile strength is equal to or more than 980MPa, and the yield strength Rp 0.2: 550-750 MPa, and the elongation after break A 80 is more than or equal to 15 percent, and the cold forming performance is good.
Drawings
FIG. 1 is a microstructure of a dual phase steel of example 1.
Detailed Description
The technical scheme of the invention is further described in detail below with reference to specific embodiments.
Examples 1 to 10
A galvanized enhanced formability dual-phase steel comprises the chemical components of ：C：0.17～0.25%,Mn：1.50～2.70%,S≤0.005%,P≤0.020%,Si：0.20～1.00%,Als：0.20～1.20%,Nb：0.02～0.080%,Cr: 0.20～1.00%, weight percent and the balance of Fe and non-removable impurities.
Preferably, the dual-phase steel comprises the following chemical components in percentage by mass ：C：0.19～0.23%,Mn：2.00～2.40%,S≤0.003%,P≤0.015%,Si：0.50～0.80%,Als：0.60～1.00%,Nb：0.020～0.050%,Cr：0.20～0.60%, and the balance of Fe and non-cleanable impurities.
The dual phase steel composition of each example is shown in Table 1.
In the composition of the components of the above examples, the balance was iron and unavoidable impurities.
The production method of the galvanized enhanced formability dual-phase steel comprises the following steps of continuous casting, heating, hot rolling, cold rolling, continuous annealing, hot galvanizing and leveling, and specifically comprises the following steps:
(1) Continuous casting process: the temperature of the tundish is 1510-1530 ℃, and the pulling speed is 1.2-1.4 m/min;
(2) Heating procedure: the heating temperature is 1200-1350 ℃, and the total heating time is 150-240 min;
(3) Hot rolling: the finish rolling temperature is 870-900 ℃ and the coiling temperature is 640-680 ℃;
(4) Cold rolling: the cold rolling reduction rate is more than or equal to 45%;
(5) And (3) a continuous annealing and hot galvanizing process, wherein the cold-rolled sheet is heated to 800-840 ℃, the heat preservation time is 60-120 s, firstly, the cold-rolled sheet is slowly cooled to 650-700 ℃, the slow cooling rate is 10-20 ℃/s, then the cold-rolled sheet is quickly cooled to 300-370 ℃, the quick cooling rate is 40-70 ℃/s, then, the temperature is increased to 450-470 ℃, the heating rate is 60-100 ℃/s, the heat preservation time is 15-30s, and then, the cold-rolled sheet enters a zinc pot, the temperature of the zinc pot is 440-460 ℃, the time of the zinc pot is 5-8 s, and the final cooling temperature is 80-150 ℃.
(6) Finishing procedure: the finishing rolling force is 2000-5000KN.
The continuous casting, heating, hot rolling and cold rolling process parameters of each embodiment are shown in Table 2; the parameters of the continuous annealing, hot galvanizing and finishing processes are shown in Table 3.
The thickness and mechanical properties of the dual phase steel of each example are shown in Table 4.
The microstructure of the dual phase steel of example 1 is shown in fig. 1, and it can be seen that the microstructure is ferrite + martensite + retained austenite.
The above embodiments are only for illustrating the technical solution of the present invention, and it should be understood by those skilled in the art that although the present invention has been described in detail with reference to the above embodiments: modifications and equivalents may be made thereto without departing from the spirit and scope of the invention, which is intended to be encompassed by the claims.

Claims (10)

1.一种镀锌增强成型性双相钢，其特征在于，所述双相钢化学成分组成及其质量百分含量为：C：0.17～0.25%，Mn：1.50～2.70%，S≤0.005%，P≤0.020%，Si：0.20～1.00%，Als：0.20～1.20%，Nb：0.02～0.080%，Cr:0.20～1.00%，其余为Fe和不可清除的杂质。1. A galvanized enhanced formability dual-phase steel, characterized in that the chemical composition and mass percentage of the dual-phase steel are: C: 0.17-0.25%, Mn: 1.50-2.70%, S≤0.005%, P≤0.020%, Si: 0.20-1.00%, Als: 0.20-1.20%, Nb: 0.02-0.080%, Cr: 0.20-1.00%, and the rest are Fe and impurities that cannot be removed. 2.根据权利要求1所述的一种镀锌增强成型性双相钢，其特征在于，所述双相钢化学成分组成及其质量百分含量为：C：0.19～0.23%，Mn：2.00～2.40%，S≤0.003%，P≤0.015%，Si：0.50～0.80%，Als：0.60～1.00%,Nb：0.020～0.050%，Cr：0.20～0.60%，其余为Fe和不可清除的杂质。2. A galvanized enhanced formable dual-phase steel according to claim 1, characterized in that the chemical composition of the dual-phase steel and its mass percentage are: C: 0.19-0.23%, Mn: 2.00-2.40%, S≤0.003%, P≤0.015%, Si: 0.50-0.80%, Als: 0.60-1.00%, Nb: 0.020-0.050%, Cr: 0.20-0.60%, and the rest are Fe and non-removable impurities. 3.根据权利要求1或2所述的一种镀锌增强成型性双相钢，其特征在于，所述冷轧连退双相钢厚度为1.0～2.2mm。3. A galvanized enhanced formability dual-phase steel according to claim 1 or 2, characterized in that the thickness of the cold-rolled and continuously annealed dual-phase steel is 1.0 to 2.2 mm. 4.根据权利要求1或2所述的一种镀锌增强成型性双相钢，其特征在于，所述冷轧连退双相钢组织由铁素体+马氏体+残余奥氏体组成。4. A galvanized enhanced formability dual-phase steel according to claim 1 or 2, characterized in that the cold-rolled and continuously annealed dual-phase steel structure consists of ferrite + martensite + retained austenite. 5.基于权利要求1-4任一项所述的一种镀锌增强成型性双相钢的生产方法，其特征在于，包括连铸、加热、热轧、冷轧、连续退火及热镀锌、光整工序。5. A method for producing galvanized enhanced formability dual-phase steel based on any one of claims 1 to 4, characterized in that it includes continuous casting, heating, hot rolling, cold rolling, continuous annealing, hot-dip galvanizing, and skin-passing steps. 6.根据权利要求5所述的一种镀锌增强成型性双相钢的生产方法，其特征在于，所述连续退火及热镀锌工序，包括将冷轧板加热至800～840℃，保温时间60～120s，先缓冷至650～700℃，缓冷冷却速率10～20℃/s，再快冷至300～370℃，快冷冷却速率40～70℃/s，随后升温至450～470℃，升温速率60～100℃/s，保温时间15-30s，后进入锌锅，锌锅温度为440～460℃，在锌锅时间5～8s，终冷温度80-150℃。6. A method for producing galvanized enhanced formable dual-phase steel according to claim 5, characterized in that the continuous annealing and hot-dip galvanizing process comprises heating the cold-rolled sheet to 800-840°C, holding time 60-120s, first slowly cooling to 650-700°C, slow cooling cooling rate 10-20°C/s, then fast cooling to 300-370°C, fast cooling cooling rate 40-70°C/s, then heating to 450-470°C, heating rate 60-100°C/s, holding time 15-30s, and then entering the zinc pot, the zinc pot temperature is 440-460°C, the zinc pot time is 5-8s, and the final cooling temperature is 80-150°C. 7.根据权利要求5所述的一种镀锌增强成型性双相钢的生产方法，其特征在于，所述连铸工序，中包温度1510～1530℃，拉速为1.2～1.4m/min。7. The method for producing a galvanized enhanced formability dual-phase steel according to claim 5, characterized in that, in the continuous casting process, the tundish temperature is 1510-1530°C and the drawing speed is 1.2-1.4 m/min. 8.根据权利要求5所述的一种镀锌增强成型性双相钢的生产方法，其特征在于，所述加热工序，加热温度为1200～1350℃，总加热时间为150～240min。8. The method for producing galvanized enhanced formability dual-phase steel according to claim 5, characterized in that, in the heating process, the heating temperature is 1200-1350°C and the total heating time is 150-240 minutes. 9.根据权利要求5所述的一种镀锌增强成型性双相钢的生产方法，其特征在于，所述热轧工序，精轧终轧温度为870-900℃，卷取温度为640～680℃。9. The method for producing a galvanized enhanced formability dual-phase steel according to claim 5, characterized in that, in the hot rolling process, the finishing rolling temperature is 870-900°C and the coiling temperature is 640-680°C. 10.根据权利要求5所述的一种镀锌增强成型性双相钢的生产方法，其特征在于，所述冷轧工序，冷轧压下率≥45%。10. The method for producing galvanized enhanced formability dual-phase steel according to claim 5, characterized in that, in the cold rolling process, the cold rolling reduction ratio is ≥45%.
CN202410695724.6A 2024-01-30 2024-05-31 A galvanized enhanced formability dual-phase steel and its production method Pending CN118256819A (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN2024101271803 2024-01-30
CN202410127180 2024-01-30

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Publication Number Publication Date
CN118256819A true CN118256819A (en) 2024-06-28

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