CN118256819A - Galvanized enhanced formability dual-phase steel and production method thereof - Google Patents
Galvanized enhanced formability dual-phase steel and production method thereof Download PDFInfo
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- 229910000885 Dual-phase steel Inorganic materials 0.000 title claims abstract description 38
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 16
- 238000010438 heat treatment Methods 0.000 claims abstract description 19
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 17
- 238000000034 method Methods 0.000 claims abstract description 15
- 238000005097 cold rolling Methods 0.000 claims abstract description 13
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 13
- 238000000137 annealing Methods 0.000 claims abstract description 12
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 11
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 11
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 10
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 9
- 238000005098 hot rolling Methods 0.000 claims abstract description 9
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 9
- 238000009749 continuous casting Methods 0.000 claims abstract description 8
- 238000005246 galvanizing Methods 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 8
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 8
- 239000000126 substance Substances 0.000 claims abstract description 8
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 7
- 238000001816 cooling Methods 0.000 claims description 18
- 230000008569 process Effects 0.000 claims description 11
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 9
- 239000011701 zinc Substances 0.000 claims description 9
- 229910052725 zinc Inorganic materials 0.000 claims description 9
- 238000005096 rolling process Methods 0.000 claims description 6
- 239000000203 mixture Substances 0.000 claims description 4
- 230000009467 reduction Effects 0.000 claims description 3
- 230000000717 retained effect Effects 0.000 claims description 3
- 229910052742 iron Inorganic materials 0.000 abstract description 4
- 229910000831 Steel Inorganic materials 0.000 description 21
- 239000010959 steel Substances 0.000 description 21
- 239000011572 manganese Substances 0.000 description 11
- 239000010955 niobium Substances 0.000 description 9
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 8
- 238000005728 strengthening Methods 0.000 description 8
- 239000011651 chromium Substances 0.000 description 7
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 6
- 229910052782 aluminium Inorganic materials 0.000 description 6
- 229910052799 carbon Inorganic materials 0.000 description 6
- 230000000694 effects Effects 0.000 description 6
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 5
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 5
- 230000009466 transformation Effects 0.000 description 5
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 4
- 239000010703 silicon Substances 0.000 description 4
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 230000000087 stabilizing effect Effects 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 230000018109 developmental process Effects 0.000 description 2
- 238000007730 finishing process Methods 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 238000004321 preservation Methods 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 230000002829 reductive effect Effects 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 125000004432 carbon atom Chemical group C* 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000003111 delayed effect Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 230000009977 dual effect Effects 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000005272 metallurgy Methods 0.000 description 1
- UNASZPQZIFZUSI-UHFFFAOYSA-N methylidyneniobium Chemical compound [Nb]#C UNASZPQZIFZUSI-UHFFFAOYSA-N 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 229910000510 noble metal Inorganic materials 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 238000007747 plating Methods 0.000 description 1
- 238000004886 process control Methods 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 238000007493 shaping process Methods 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 239000002436 steel type Substances 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
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
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. The galvanized enhanced formability dual-phase steel is characterized in that the chemical composition of the dual-phase steel and the mass percentage content thereof 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 balance is Fe and non-removable impurities.
2. The galvanized enhanced formability dual phase steel according to claim 1, wherein the dual phase steel has a chemical composition 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%, mass% and the balance being Fe and non-removable impurities.
3. The galvanization reinforced formability dual phase steel according to claim 1 or 2, wherein the cold rolling continuous annealing dual phase steel has a thickness of 1.0-2.2 mm.
4. The galvanization enhanced formability dual phase steel according to claim 1 or 2, wherein the cold rolling continuous annealing dual phase steel structure is composed of ferrite + martensite + retained austenite.
5. A method for producing a galvanized enhanced formability dual phase steel according to any one of claims 1 to 4, comprising continuous casting, heating, hot rolling, cold rolling, continuous annealing, hot galvanizing, and finishing steps.
6. The method for producing a dual-phase steel with enhanced galvanization and formability according to claim 5, wherein the continuous annealing and hot galvanizing process comprises heating a cold rolled sheet to 800-840 ℃, keeping the temperature for 60-120 s, slowly cooling to 650-700 ℃, slowly cooling to 10-20 ℃/s, rapidly cooling to 300-370 ℃, rapidly cooling to 40-70 ℃/s, then heating to 450-470 ℃, heating to 60-100 ℃/s, keeping the temperature 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 ℃.
7. The method for producing a galvanized enhanced formability dual phase steel according to claim 5, wherein the continuous casting process has a tundish temperature of 1510-1530 ℃ and a drawing speed of 1.2-1.4 m/min.
8. The method for producing a galvanized enhanced formability dual phase steel according to claim 5, wherein the heating process is performed at 1200-1350 ℃ for 150-240 min.
9. The method for producing a galvanized enhanced formability dual phase steel according to claim 5, wherein the hot rolling process has a finish rolling temperature of 870-900 ℃ and a coiling temperature of 640-680 ℃.
10. The method for producing a galvanized enhanced formability dual phase steel according to claim 5, wherein the cold rolling process has a cold rolling reduction of 45% or more.
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2024101271803 | 2024-01-30 |
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| CN118256819A true CN118256819A (en) | 2024-06-28 |
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