CN115710673B - High-reaming cold-rolled DH1180 steel and preparation method thereof - Google Patents
High-reaming cold-rolled DH1180 steel and preparation method thereof Download PDFInfo
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Abstract
The invention provides a high-reaming cold-rolled DH1180 steel and a preparation method thereof, wherein the steel comprises the following components in percentage by weight: c:0.15 to 0.25 percent of Mn:1.80 to 2.80 percent, si:0.20 to 2.00 percent of Al:0.5 to 5.0 percent, P is less than or equal to 0.01 percent, S is less than or equal to 0.01 percent, N is less than or equal to 0.005 percent, ti:0.010 to 0.150 percent, ca:0.005% -0.150%, mg:0.002% -0.150%, wherein Al/Si:1.0 to 3.0; C/Ti:2 to 10; ca+Mg:0.05 to 0.20 percent; the balance of Fe and unavoidable impurities; the preparation method comprises the steps of converter smelting, continuous casting and rolling of medium-thin slabs, pickling and cold rolling, continuous annealing and finishing; the yield strength of the steel produced by the invention is more than or equal to 850MPa, the tensile strength is 1180-1300 MPa, the elongation after A50 breaking is more than or equal to 15%, and the reaming ratio is more than or equal to 30%; meets the requirements of low cost and excellent extensibility and formability of automobiles.
Description
Technical Field
The invention belongs to the field of metal materials, and particularly relates to a short-flow low-cost high-reaming cold-rolled DH1180 steel and a preparation method thereof.
Background
In the automotive industry, higher requirements have been put on the weight reduction, emission limitation and safety standards of the car body, and in order to better serve users, the automotive industry has increasingly demanded parts with high formability. The conventional dual-phase steel is difficult to meet the requirement of high-ductility complex cup punching, and the TRIP steel is limited to be widely used due to high alloy content and high production cost. DH steel is an English abbreviation of Dual Phase Steels with Improved Formability and is first mentioned by the VDA239-100 cold-formed steel sheet standard published by the German automobile industry Association in 2016. DH steel has good formability due to the introduction of a certain amount of retained austenite, and can overcome the defects of DP steel and TRIP steel in the application process, so that the DH steel has remarkable advantages in the future steel application market.
Patent document CN112095046B discloses an ultra-high strength cold rolled DH1180 steel and a preparation method thereof, the main chemical components of which are: c:0.18 to 0.25 percent of Mn:1.8 to 2.8 percent, si:0.5 to 1.4 percent of Al:0.02% -1.4%, cr:0.03 to 0.60 percent, mo:0.04 to 0.4 percent of Ti:0.002% -0.1%, P is less than or equal to 0.03%, S is less than or equal to 0.03%, V is less than or equal to 0.05%, nb is less than or equal to 0.1%, and Si+Al:0.8% -2.0%, mo+Ti:0.10 to 0.50 percent, and the balance of iron and unavoidable impurities. The cold-rolled DH steel with the strength grade of 1180MPa is excellent in hydrogen embrittlement resistance and forming performance, however, the alloy cost of the product is obviously improved by using a large amount of noble metals such as Cr, mo, nb and V, and the production process is very complex and tedious by adopting the traditional cold rolling-continuous annealing process.
Patent document CN113403550A discloses a cold-rolled hot-dip galvanized DH1180 steel plate with high plasticity and fatigue resistance and a preparation method thereof, wherein the main chemical components are as follows: c:0.16 to 0.25 percent of Mn:1.8 to 2.6 percent, si:0.2 to 0.8 percent of Al:0.50 to 1.5 percent, 0.10 to 0.60 percent of Cr, 0.10 to 0.70 percent of Cu, less than or equal to 0.01 percent of P, less than or equal to 0.01 percent of S, less than or equal to 0.003 percent of N, and Nb:0.005% -0.15%, V:0.005% -0.15%, ti:0.005% -0.15%, and the balance of iron and unavoidable impurities. The cold-rolled hot-dip galvanized DH steel with the strength grade of 1180MPa is excellent in plasticity and fatigue resistance service performance, however, the alloy cost of the product is obviously improved by using a large amount of noble metals such as Cr, cu, nb and V, and the traditional cold-rolled hot-dip galvanized production process is adopted.
Disclosure of Invention
The invention aims to overcome the problems and the shortcomings and provide the high-reaming cold-rolled DH1180 steel which can reduce the alloy cost and shorten the production flow of the traditional production line while meeting the basic performance index of the product, and the preparation method thereof.
The invention aims at realizing the following steps:
a high-reaming cold-rolled DH1180 steel comprises the following components in percentage by weight: c:0.15 to 0.25 percent of Mn:1.80 to 2.80 percent, si:0.20 to 2.00 percent of Al:0.5 to 5.0 percent, P is less than or equal to 0.01 percent, S is less than or equal to 0.01 percent, N is less than or equal to 0.005 percent, ti:0.010 to 0.150 percent, ca:0.005% -0.150%, mg:0.002% -0.150%, wherein Al/Si:1.0 to 3.0; C/Ti:2 to 10; ca+Mg:0.05 to 0.20 percent; the balance being Fe and unavoidable impurities.
The yield strength of the steel is more than or equal to 850MPa, the tensile strength is 1180-1300 MPa, the elongation after A50 breaking is more than or equal to 15%, and the reaming ratio is more than or equal to 30%; meets the requirements of low cost and excellent extensibility and formability of automobiles.
The microstructure of the steel is ferrite, martensite and residual austenite; wherein, the above-mentioned organization is as follows by the volume percent: 10-40% of ferrite, 50-80% of martensite and 4-15% of residual austenite.
The reason for designing the components of the invention is as follows:
c: the carbon element guarantees the strength requirement of the steel through solid solution strengthening, and sufficient carbon element helps to stabilize austenite, so that the forming performance of the steel is improved. The content of the element C is too low to obtain the mechanical properties of the steel in the invention; too high a content can embrittle the steel and present a risk of delayed fracture. Therefore, the content of the C element is controlled to be 0.15-0.25%.
Mn: manganese is an austenite stabilizing element in steel, can enlarge an austenite phase region, reduce the critical quenching speed of the steel, and can refine grains, thereby being beneficial to solid solution strengthening to improve the strength. The content of Mn element is too low, supercooled austenite is not stable enough, and the plasticity, toughness and other processing performances of the steel plate are reduced; the too high Mn content can cause the poor welding performance of the steel plate, and the production cost is increased, which is not beneficial to industrial production. Therefore, the Mn element content is controlled to be 1.80-2.80% in the invention.
Si: the Si element has certain solid solution strengthening effect in ferrite, so that the steel has enough strength, and meanwhile, si can inhibit the decomposition of residual austenite and the precipitation of carbide, so that the inclusions in the steel are reduced. The Si element content is too low to play a role in strengthening; the excessively high content of Si element may deteriorate the surface quality and weldability of the steel sheet. Therefore, the content of Si element is controlled to be 0.20% to 2.00% in the present invention.
Al: the aluminum element contributes to deoxidization of the molten steel. The method can also inhibit the decomposition of residual austenite and the precipitation of carbide, and accelerate the transformation of bainite to improve the coordination deformation capability. The content of Al element is too high, which not only increases the production cost, but also causes difficult continuous casting production and the like. Therefore, the content of the Al element is controlled to be 0.50-5.00 percent, and the content of the Al element meets the following conditions: 1.0 to 3.0.
P: the P element is a harmful element in steel, the plasticity and the deformability of the steel are seriously reduced, and the lower the content is, the better the steel is. In consideration of cost, the content of the P element is controlled to be less than or equal to 0.01 percent.
S: the S element is a harmful element in steel, seriously affecting the formability of the steel, and the lower the content is, the better. In view of cost, the content of S element is controlled to be less than or equal to 0.01 percent.
N: the N element is a harmful element in the steel, seriously affects the comprehensive performance of the steel, and the lower the content is, the better the content is. In view of cost, the content of N element is controlled to be less than or equal to 0.005 percent.
Ti: the microalloying element Ti improves the comprehensive performance of the material through fine crystal strengthening and precipitation strengthening, and in order to control the production cost, the content of the Ti element is controlled to be 0.010-0.150 percent, and the content of C/Ti is 2-10.
Ca: the addition of a small amount of Ca element is because Ca element has low price, and the Ca element can be used as a deoxidizer and an inoculant when being added into a master alloy, thereby playing a role of microalloying, further obviously refining grains and improving the comprehensive properties of steel such as plasticity, welding performance and the like; meanwhile, ca element has good desulfurization effect, can change the components, quantity and form of nonmetallic inclusion, can improve the hydrogen-induced crack resistance and lamellar tearing resistance, and can prolong the service life of parts. In order to control the production cost, the content of Ca element is controlled to be 0.005-0.150 percent.
Mg: magnesium is a good deoxidizer, desulfurizing agent and nodulizer in steel, and Mg can reduce the number of inclusions in steel, reduce the size, uniformly distribute and improve the shape. The trace magnesium can improve the carbide size and distribution of DH steel and promote the tiny and uniform carbide particles. In order to control the production cost, the content of Mg element is controlled to be 0.002% -0.150%, and Ca and Mg elements are used in a matching way, so that the content of Ca+Mg is satisfied: 0.05 to 0.20 percent.
The second technical scheme of the invention is to provide a preparation method of high-reaming cold-rolled DH1180 steel, which comprises converter smelting, continuous casting and rolling of medium-thin slabs, pickling and cold rolling, continuous annealing and finishing;
smelting in a converter: smelting by a converter to obtain molten steel which meets the following component requirements in percentage by mass: 0.15 to 0.25 percent of Mn:1.80 to 2.80 percent, si:0.20 to 2.00 percent of Al:0.5 to 5.0 percent, P is less than or equal to 0.01 percent, S is less than or equal to 0.01 percent, N is less than or equal to 0.005 percent, ti:0.010 to 0.150 percent, ca:0.005% -0.150%, mg:0.002% -0.150%, wherein Al/Si:1.0 to 3.0; C/Ti:2 to 10; ca+Mg:0.05 to 0.20 percent; the balance of Fe and unavoidable impurities, and the temperature of molten steel is 1600-1700 ℃.
Continuous casting and rolling of medium thin slabs: the casting temperature is 1530-1580 ℃, the drawing speed of the casting machine is 0.8-3.0 m/min, and the thickness of the continuous casting billet is 60-115 mm. The casting blank is directly put into a furnace after being pulled out and cut, the heating temperature is controlled to be 1100-1300 ℃, the heat preservation time is 30-120 min, the initial rolling temperature is 1000-1150 ℃, the final rolling temperature is 800-900 ℃, and the coiling temperature is 500-600 ℃. The thickness specification of the hot rolled steel plate is 2.0-4.5 mm, and the microstructure of the hot rolled steel plate consists of 20-50% (volume ratio) ferrite, 30-60% (volume ratio) pearlite, 10-30% (volume ratio) bainite and a small amount of cementite; the sum is 100%.
Acid pickling cold rolling: the oxidized iron scales on the surface of the hot rolled steel coil are removed by acid liquor before cold rolling, and the cold rolling reduction rate is 40% -60%. Too high a reduction ratio can result in too high deformation resistance, and is difficult to roll to a target thickness; too low rolling reduction may cause a decrease in elongation of the cold-rolled steel sheet.
Continuous annealing: the belt speed is controlled at 60-150 m/min, the soaking section temperature is 800-950 ℃, the soaking time is 10-600 s, the slow cooling outlet temperature is 700-760 ℃, the rapid cooling rate is more than 30 ℃/s, and the rapid cooling outlet temperature is 300-450 ℃;
and (3) finishing: the rolling force is controlled to be 2000-4000 kN and the rolling tension is 1000-2000 kN.
The microstructure of the cold rolling continuous annealing product is 10% -40% ferrite, 50% -80% martensite and 4% -15% retained austenite. The temperature of the soaking section is 800-950 ℃, if the temperature of the soaking section is too high, the austenitizing tends to be complete, and the ferrite proportion is insufficient, so that the ductility of the steel is reduced; if the annealing temperature is too low, the strength of the material is greatly reduced by too high a proportion of soft-phase ferrite of the final material. The soaking time is 10-600 s, if the soaking time is too long, the steel plate grains are coarse, the annealing time is too short, the annealing and recrystallization processes of the steel plate are not completed rapidly, and the elongation of the steel plate is reduced.
The high-reaming cold-rolled DH1180 steel can be obtained by the method, the yield strength is more than or equal to 850MPa, the tensile strength is 1180-1300 MPa, the elongation after A50 breaking is more than or equal to 15%, and the reaming ratio is more than or equal to 30%.
The invention has the beneficial effects that:
(1) The high-reaming cold-rolled DH1180 steel produced by the invention is prepared by optimizing the design of alloy components, taking C, mn and Si as main elements, and adding no noble metal elements such as Cr, mo, nb, V and the like, and has very low alloy cost.
(2) The high-reaming cold-rolled DH1180 steel produced by the invention adopts a production process of converter smelting, medium-thin slab continuous casting and rolling, pickling cold rolling, continuous annealing and finishing, and can realize industrial production of the DH980 steel for automobiles on a traditional production line without adding new production equipment; however, the invention replaces the original continuous casting-hot feeding-hot charging-heating-hot rolling-coiling process and saves the aging process in the continuous annealing process by the continuous casting and rolling process of the medium sheet billet, obviously shortens the DH steel process flow, ensures stable production and greatly reduces the manufacturing cost of the product.
(3) The yield strength of the high-reaming cold-rolled DH1180 steel prepared by the method is equal to or more than 850MPa, the tensile strength is 1180-1300 MPa, the elongation after A50 breaking is equal to or more than 15%, the reaming ratio is equal to or more than 30%, and the advantages of ensuring the short flow and low cost of the product, and simultaneously achieving excellent plasticity, reaming performance and the like are achieved.
(4) The high-reaming cold-rolled DH1180 steel produced by the invention is characterized in that a certain proportion of residual austenite is added on the basis of the traditional cold-rolled dual-phase steel, and the high ductility and the high forming performance of the steel are realized under the action of transformation induced plasticity (TRIP) effect.
(5) The microstructure volume percentage of the high-reaming cold-rolled DH1180 steel hot-rolled steel plate produced by the invention is as follows: 20-50% of ferrite, 30-60% of pearlite, 10-30% of bainite and the balance of a small amount of cementite; the sum is 100%; the microstructure of the cold rolling continuous annealing product is 10% -40% ferrite, 50% -80% martensite and 4% -15% retained austenite, and the total is 100%.
Drawings
FIG. 1 is a typical engineering stress strain curve for inventive steel example 1.
Detailed Description
The invention is further illustrated by the following examples.
According to the component proportion of the technical scheme, the embodiment of the invention carries out converter smelting, continuous casting and rolling of medium-thin slabs, pickling and cold rolling, continuous annealing and finishing.
Smelting in a converter: the temperature of molten steel is 1600-1700 ℃;
continuous casting and rolling of medium thin slabs: the casting temperature is 1530-1580 ℃, the drawing speed of a casting machine is 0.8-3.0 m/min, and the thickness of a continuous casting billet is 60-115 mm; directly feeding the casting blank into a furnace after pulling and cutting, controlling the heating temperature to 1100-1300 ℃, the heat preservation time to 30-120 min, the initial rolling temperature to 1000-1150 ℃, the final rolling temperature to 800-900 ℃ and the coiling temperature to 500-600 ℃;
acid pickling cold rolling: the cold rolling reduction rate is 40% -60%;
continuous annealing: the belt speed is controlled to be 60-150 m/min, the soaking section temperature is 800-950 ℃, the soaking time is 10-600 s, the slow cooling outlet temperature is 700-760 ℃, the rapid cooling rate is more than 30 ℃/s, and the rapid cooling outlet temperature is 300-450 DEG C
And (3) finishing: the rolling force in the finishing process is controlled to be 2000-4000 kN, and the rolling tension is 1000-2000 kN.
Further; the thickness of the hot rolled steel plate after continuous casting and rolling of the medium sheet billet is 2.0-4.5 mm, and the microstructure of the hot rolled steel plate is ferrite, pearlite, bainite and a small amount of cementite; the organization safety price percentage is as follows: 20-50% of ferrite, 30-60% of pearlite, 10-30% of bainite and a small amount of cementite in balance.
The composition of the steel of the example of the invention is shown in Table 1. The main technological parameters of the continuous casting and rolling of the steel of the embodiment of the invention are shown in table 2. The main technological parameters of the cold rolling annealing of the steel of the embodiment of the invention are shown in Table 3. The properties of the inventive example steels are shown in Table 4. The microstructure of the steel of the invention is shown in Table 5.
TABLE 1 composition (wt%) of the inventive example steel
| Examples | C | Mn | Si | Al | Al/Si | P | S | N | Ti | C/Ti | Ca | Mg | Ca+Mg |
| 1 | 0.18 | 2.31 | 0.32 | 0.76 | 2.4 | 0.002 | 0.003 | 0.002 | 0.031 | 5.8 | 0.012 | 0.043 | 0.055 |
| 2 | 0.21 | 2.04 | 0.47 | 0.81 | 1.7 | 0.008 | 0.001 | 0.001 | 0.025 | 8.4 | 0.035 | 0.067 | 0.102 |
| 3 | 0.20 | 1.89 | 0.78 | 1.28 | 1.6 | 0.004 | 0.004 | 0.001 | 0.048 | 4.2 | 0.072 | 0.028 | 0.100 |
| 4 | 0.23 | 1.81 | 0.86 | 2.41 | 2.8 | 0.001 | 0.001 | 0.002 | 0.052 | 4.4 | 0.127 | 0.052 | 0.179 |
| 5 | 0.17 | 2.27 | 0.67 | 0.98 | 1.5 | 0.003 | 0.002 | 0.001 | 0.071 | 2.4 | 0.046 | 0.043 | 0.089 |
| 6 | 0.16 | 2.16 | 1.23 | 3.18 | 2.6 | 0.004 | 0.001 | 0.002 | 0.038 | 4.2 | 0.053 | 0.038 | 0.091 |
| 7 | 0.22 | 1.83 | 0.58 | 1.21 | 2.1 | 0.003 | 0.003 | 0.001 | 0.027 | 8.1 | 0.112 | 0.014 | 0.126 |
| 8 | 0.24 | 2.09 | 0.49 | 0.56 | 1.1 | 0.004 | 0.002 | 0.001 | 0.043 | 5.6 | 0.072 | 0.023 | 0.095 |
| 9 | 0.15 | 2.43 | 1.84 | 4.32 | 2.3 | 0.005 | 0.004 | 0.001 | 0.044 | 3.4 | 0.142 | 0.034 | 0.176 |
Note that: C/Ti and Al/Si non-unit
TABLE 2 main process parameters of continuous casting and rolling of the inventive example steel
TABLE 3 Main Process parameters for Cold annealing of example steels according to the invention
TABLE 4 Properties of the inventive example Steel
TABLE 5 microstructure of the inventive steels
The high-reaming cold-rolled DH1180 steel prepared by the method has the advantages that the yield strength is more than or equal to 850MPa, the tensile strength is 1180-1300 MPa, the elongation after A50 breaking is more than or equal to 15%, the reaming ratio is more than or equal to 30%, and the advantages of excellent plasticity, reaming performance and the like are simultaneously achieved while the short flow and low cost of the product are ensured.
The present invention has been properly and fully described in the foregoing embodiments by way of example only, and not by way of limitation, and various changes and modifications may be made by one skilled in the art without departing from the spirit and scope of the invention, any modification, equivalent substitution, improvement, etc. should be included in the scope of the invention, and the scope of the invention is defined by the claims.
Claims (4)
1. The high-reaming cold-rolled DH1180 steel is characterized by comprising the following components in percentage by weight: c:0.15 to 0.25 percent of Mn:1.80 to 2.80 percent, si:0.20 to 2.00 percent of Al:2.41 to 5.0 percent, P is less than or equal to 0.01 percent, S is less than or equal to 0.01 percent, N is less than or equal to 0.005 percent, ti:0.010 to 0.150 percent, ca:0.005% -0.150%, mg:0.002% -0.150%, wherein Al/Si:1.0 to 3.0; C/Ti:2 to 10; ca+Mg:0.05 to 0.20 percent; the balance of Fe and unavoidable impurities; the microstructure of DH1180 steel is ferrite, martensite and retained austenite; wherein, the above-mentioned organization is as follows by the volume percent: 10-40% of ferrite, 50-80% of martensite and 4-15% of residual austenite.
2. The high-reaming cold-rolled DH1180 steel of claim 1, wherein the steel has a yield strength of not less than 850MPa, a tensile strength of 1180-1300 MPa, an elongation after A50 break of not less than 15% and a reaming ratio of not less than 30%.
3. A method for preparing a high-reaming cold-rolled DH1180 steel as claimed in claim 1 or 2, comprising converter smelting, continuous casting and rolling of medium sheet billet, pickling and cold rolling, continuous annealing and finishing; the method is characterized in that:
smelting in a converter: the temperature of molten steel is 1600-1700 ℃;
continuous casting and rolling of medium thin slabs: the casting temperature is 1530-1580 ℃, the drawing speed of a casting machine is 0.8-3.0 m/min, and the thickness of a continuous casting billet is 60-115 mm; directly feeding the casting blank into a furnace after pulling and cutting, controlling the heating temperature to 1100-1194 ℃, the heat preservation time to 30-120 min, the initial rolling temperature to 1000-1150 ℃, the final rolling temperature to 800-893 ℃ and the coiling temperature to 500-600 ℃;
acid pickling cold rolling: the cold rolling reduction rate is 40% -60%;
continuous annealing: the belt speed is controlled at 60-150 m/min, the soaking section temperature is 800-950 ℃, the soaking time is 10-600 s, the slow cooling outlet temperature is 700-760 ℃, the rapid cooling rate is more than 30 ℃/s, and the rapid cooling outlet temperature is 300-450 ℃;
and (3) finishing: the rolling force in the finishing process is controlled to be 2000-4000 kN, and the rolling tension is 1000-2000 kN.
4. The method for preparing the high-reaming cold-rolled DH1180 steel according to claim 3, wherein the steps of: the thickness of the hot rolled steel plate after continuous casting and rolling of the medium sheet billet is 2.0-4.5 mm, and the microstructure of the hot rolled steel plate is ferrite, pearlite, bainite and a small amount of cementite; the above-mentioned tissue is as follows by volume percent: 20-50% of ferrite, 30-60% of pearlite, 10-30% of bainite and a small amount of cementite in balance.
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| US20230399727A1 (en) * | 2021-04-27 | 2023-12-14 | Nippon Steel Corporation | Steel sheet and plated steel sheet |
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| CN113403550B (en) * | 2021-05-21 | 2022-08-16 | 鞍钢股份有限公司 | High-plasticity fatigue-resistant cold-rolled hot-galvanized DH1180 steel plate and preparation method thereof |
| CN113403545B (en) * | 2021-05-21 | 2022-07-22 | 鞍钢股份有限公司 | High-hole-expansibility DH1180MPa cold-rolled continuous-annealing steel plate and preparation method thereof |
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