CN113737086A - Economical 780 MPa-grade cold-rolled annealed dual-phase steel and manufacturing method thereof - Google Patents
Economical 780 MPa-grade cold-rolled annealed dual-phase steel and manufacturing method thereof Download PDFInfo
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- 229910000885 Dual-phase steel Inorganic materials 0.000 title claims abstract description 63
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 27
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 57
- 239000010959 steel Substances 0.000 claims abstract description 57
- 238000000137 annealing Methods 0.000 claims abstract description 32
- 238000001816 cooling Methods 0.000 claims abstract description 21
- 238000005452 bending Methods 0.000 claims abstract description 18
- 238000005097 cold rolling Methods 0.000 claims abstract description 14
- 238000002791 soaking Methods 0.000 claims abstract description 13
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 11
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 10
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 10
- 229910052729 chemical element Inorganic materials 0.000 claims abstract description 9
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 8
- 238000005496 tempering Methods 0.000 claims abstract description 7
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 7
- 238000005098 hot rolling Methods 0.000 claims abstract description 6
- 238000003723 Smelting Methods 0.000 claims abstract description 4
- 238000009749 continuous casting Methods 0.000 claims abstract description 4
- 239000011159 matrix material Substances 0.000 claims abstract description 3
- 238000000034 method Methods 0.000 claims description 14
- 229910052758 niobium Inorganic materials 0.000 claims description 11
- 229910052698 phosphorus Inorganic materials 0.000 claims description 8
- 239000012535 impurity Substances 0.000 claims description 7
- 229910052757 nitrogen Inorganic materials 0.000 claims description 7
- 230000009467 reduction Effects 0.000 claims description 7
- 229910052717 sulfur Inorganic materials 0.000 claims description 7
- 238000012512 characterization method Methods 0.000 claims description 6
- 238000013461 design Methods 0.000 description 11
- 230000000052 comparative effect Effects 0.000 description 9
- 229910045601 alloy Inorganic materials 0.000 description 8
- 239000000956 alloy Substances 0.000 description 8
- 229910052799 carbon Inorganic materials 0.000 description 7
- 239000000203 mixture Substances 0.000 description 7
- 230000008569 process Effects 0.000 description 6
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- 238000007670 refining Methods 0.000 description 3
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- 229910000914 Mn alloy Inorganic materials 0.000 description 2
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- 239000013078 crystal Substances 0.000 description 2
- 230000009977 dual effect Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 150000004767 nitrides Chemical class 0.000 description 2
- 238000011056 performance test Methods 0.000 description 2
- 230000002829 reductive effect Effects 0.000 description 2
- -1 C: 0.14 to 0.21% Inorganic materials 0.000 description 1
- 229910000742 Microalloyed steel Inorganic materials 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
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- 238000010438 heat treatment Methods 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
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- 238000011112 process operation Methods 0.000 description 1
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- 238000003908 quality control method Methods 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- B21C47/00—Winding-up, coiling or winding-off metal wire, metal band or other flexible metal material characterised by features relevant to metal processing only
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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Abstract
The invention discloses economical 780 MPa-grade cold-rolled annealed dual-phase steel, the matrix structure of which is fine and uniform martensite and ferrite, and the cold-rolled annealed dual-phase steel contains the following chemical elements in percentage by mass: c: 0.1% -0.13%, Si: 0.4-0.8%, Mn: 1.65% -1.9%, Al: 0.01 to 0.05 percent, Nb: 0.01-0.03%, Ti: 0.01-0.03%; and the cold-rolled annealed dual-phase steel does not contain Cr and Mo elements. In addition, the invention also discloses a manufacturing method of the cold-rolled annealed dual-phase steel, which comprises the following steps: (1) smelting and continuous casting (2), hot rolling (3), cold rolling (4) and annealing: the annealing soaking temperature is 770-820 ℃, the annealing time is 40-200 s, then the steel is cooled to the rapid cooling starting temperature at the speed of 3-5 ℃/s, and then the steel is rapidly cooled at the speed of 30-80 ℃/s, wherein the rapid cooling starting temperature is 650-730 ℃, and the rapid cooling ending temperature is 200-270 ℃; (5) tempering; (6) and (7) flattening. The cold-rolled annealed dual-phase steel has the characteristics of high strength, excellent elongation and cold bending property.
Description
Technical Field
The invention relates to a metal material and a manufacturing method thereof, in particular to cold-rolled annealed dual-phase steel and a manufacturing method thereof.
Background
With the global energy crisis and the aggravation of environmental issues, energy conservation and safety have become the major development directions in the automobile industry. Among them, reducing the vehicle weight is one of measures for energy saving and emission reduction. The high-strength dual-phase steel has good mechanical property and service performance, and can be effectively suitable for production and manufacturing of vehicle structural members.
With the development of ultra-high strength steel and the change of the current market, the ultra-high strength steel is expected to have economical type and better performance. At present, 780DP steel is still the mainstream steel, accounts for 60 percent of the total weight of the DP steel, and is widely applied to various types of structural parts and safety parts. With the continuous development of the weight-reducing and energy-saving trend of the automobile industry, rapid progress of the steel mill level at home and abroad, particularly at home and abroad, the development of future dual-phase steel is bound to be mainly integrated with low cost and high performance.
Canadian patent document No. CA2526488, published as 2004, 12.2, entitled "cold rolled steel sheet having local plasticity of 780MPA or higher and suppressing increase in weld hardness", discloses a cold rolled steel sheet whose chemical composition is: c: 0.05-0.09%; si: 0.4-1.3%; mn: 2.5-3.2%; mo can be optionally added: 0.05-0.5% or Ni: 0.05-2%; p: 0.001-0.05%; s is less than or equal to 0.08 × Ti-3.43 × N + 0.004; n is less than or equal to 0.006 percent; al: 0.005-0.10%; ti: 0.001-0.045%, and Nb is less than or equal to 0.04% or B: 0.0002 to 0.0015 percent of Ca can be added for treatment; others are Fe and unavoidable impurities. The bainite content is required to be more than 7 percent, Pcm is required to be less than or equal to 0.3, hot rolling is carried out at the temperature of more than Ar3, coiling is carried out at the temperature of below 700 ℃, cold rolling and annealing are carried out at the temperature of 700-900 ℃, rapid cooling is carried out at the temperature of 550-700 ℃, and finally high-strength steel with the strength of 780Mpa at the minimum is obtained. The steel has the characteristics of strong local deformation capability and low hardness of a welding area. However, the steel is designed to have a high Mn content, which inevitably causes a serious band-shaped structure, thereby causing non-uniformity of mechanical properties. In addition, when high Mn is added, relatively large amounts of Si are added, which is disadvantageous in both the surface quality and weldability of the steel.
U.S. patent publication No. US20050167007, published as 8/4/2005, discloses a method for manufacturing a high-strength steel sheet, which comprises the following chemical components: 0.05-0.13% of C, 0.5-2.5% of Si, 0.5-3.5% of Mn, 0.05-1% of Cr, 0.05-0.6% of Mo, less than or equal to 0.1% of Al, less than or equal to 0.005% of S, less than or equal to 0.01% of N, less than or equal to 0.03% of P, and 0.005-0.05% of Ti, 0.005-0.05% of Nb or 0.005-0.2% of V. The steel is hot rolled above Ar3 temperature, coiled at 450-700 ℃, annealed, cooled and quenched from 700-600 ℃ at the cooling rate of 100 ℃/s, and then tempered at 180-450 ℃, and finally the high-strength steel with the tensile strength of 780Mpa and the hole expansion rate of more than 50% is obtained. The main problems of the steel are that the total alloy content is too high, the Si content is high, and the weldability and the phosphorization performance of the steel are not favorable.
Chinese patent publication No. CN101363099A, published as 2009, 2, 11, entitled "a cold-rolled dual-phase steel sheet with 1000MPA tensile strength and method for manufacturing the same", discloses an ultra-high strength dual-phase steel, including C: 0.14 to 0.21%, Si: 0.4 to 0.9%, Mn: 1.5-2.1%, P: not more than 0.02%, not more than 0.01%, Nb: 0.001-0.05%, V: 0.001-0.02%, hot rolling and cold rolling, and then preserving heat at 760-820 ℃, wherein the cooling speed is 40-50 ℃/s, and overaging is carried out for 180-300 s at 240-320 ℃. The steel has high carbon equivalent design and does not have the characteristic of balanced performance.
Therefore, although the prior patent technology for designing 780MPa dual-phase steel relates to better formability, the prior patent technology adopts high C content and high Si content or contains more Cr, Ni, Mo and other alloy contents, which are not beneficial to the weldability, the surface quality and the phosphorization performance of the steel and have higher cost. In addition, some steels with high Si content have a high hole expansion ratio and good bending properties, but have a high yield ratio and reduced punching properties.
Disclosure of Invention
One of the purposes of the invention is to provide economical 780MPa grade cold-rolled annealed dual-phase steel, which enables the strength of the obtained steel plate to reach 780MPa grade through reasonable design of alloy elements and a manufacturing process on the premise of not adding Mo and Cr, obtains fine and uniform martensite + ferrite dual-phase structure to ensure that the elongation and the cold bending performance are excellent, and has better formability. The yield strength of the cold-rolled annealed dual-phase steel is more than or equal to 420 MPa; the tensile strength is more than 780 MPa; a. the50The gauge length fracture elongation is more than or equal to 18 percent; the 90-degree cold bending performance characterization parameter R/t is less than or equal to 1, wherein R represents the bending radius, t represents the plate thickness, and the unit parameter is mm.
In order to achieve the aim, the invention provides an economical 780MPa grade cold-rolled annealed dual-phase steel, the matrix structure of which is fine and uniform martensite + ferrite, and the cold-rolled annealed dual-phase steel also comprises the following chemical elements in percentage by mass besides Fe:
C：0.1％～0.13％，Si：0.4％～0.8％，Mn：1.65％～1.9％，Al：0.01％～0.05％，Nb：0.01～0.03％，Ti：0.01～0.03％；
and the cold-rolled annealed dual-phase steel does not contain Cr and Mo elements.
Further, in the cold-rolled annealed dual-phase steel of the present invention, the chemical elements thereof are, by mass:
c: 0.1% -0.13%, Si: 0.4-0.8%, Mn: 1.65% -1.9%, Al: 0.01 to 0.05 percent, Nb: 0.01-0.03%, Ti: 0.01-0.03%, and the balance of Fe and other inevitable impurities.
In the cold-rolled annealed dual-phase steel, the component system mainly comprising C, Mn is designed, so that the strength of the cold-rolled annealed dual-phase steel can reach 780MPa, and the steel can effectively ensure economy without adding noble alloy elements such as Mo, Cr and the like. The trace addition of Nb and Ti can achieve the effect of inhibiting the growth of austenite grains and can effectively refine the grains. The special component design of Mo and Cr is not added, so that the strength of the hot-rolled coil is not too high, and the manufacturability of cold rolling can be ensured. The design principle of each chemical element is as follows:
c: in the cold-rolled annealed dual-phase steel of the present invention, the addition of the element C can improve the strength of the steel and the hardness of martensite. If the mass percentage of C in the steel is less than 0.1%, the strength of the steel sheet is affected and the formation amount and stability of austenite are not facilitated; when the mass percentage of C in the steel is higher than 0.13%, the martensite hardness is too high, the grain size is large, which is not favorable for the formability of the steel plate, and the carbon equivalent is too high, which is not favorable for welding. Therefore, the mass percent of C in the cold rolling annealing dual-phase steel is controlled between 0.1 percent and 0.13 percent.
In some preferred embodiments, the mass percentage of C may be controlled between 0.11% and 0.125%.
Si: in the cold-rolled annealed dual-phase steel of the present invention, the hardenability can be improved by adding Si element to the steel. Moreover, Si dissolved in the steel can affect the interaction of dislocation, thereby increasing the work hardening rate, properly improving the elongation in the dual-phase steel, and being beneficial to obtaining better formability. However, it should be noted that if the mass percentage of Si in the steel is too high, the surface quality control is not favorable. Therefore, the mass percent of Si in the cold rolling annealing dual-phase steel is controlled between 0.4 percent and 0.8 percent.
In some preferred embodiments, the mass percentage of Si may be controlled between 0.5% and 0.7%.
Mn: in the cold-rolled annealed dual-phase steel, Mn element is added, so that the hardenability of the steel is improved, and the strength of a steel plate can be effectively improved. However, it should be noted that when the mass percentage of Mn in the steel is less than 1.65%, the strength of the steel sheet is insufficient; when the mass percentage of Mn in the steel is more than 1.9%, the strength of the steel sheet is excessively high, so that the formability thereof is deteriorated. Therefore, the mass percent of Mn in the cold-rolled annealed dual-phase steel is controlled to be between 1.65 and 1.9 percent.
In some preferred embodiments, the mass percentage of Mn may be controlled between 1.7% and 1.8%.
Al: in the cold-rolled annealed dual-phase steel, the addition of the Al element can play a role in deoxidation and grain refinement. The mass percent of Al in the cold rolling annealing dual-phase steel is controlled between 0.01 percent and 0.05 percent.
In some preferred embodiments, the mass percentage of Al may be controlled between 0.015% and 0.045%.
Nb: in the cold rolling annealing dual-phase steel, Nb is an important element for refining grains, and after a small amount of strong carbide forming element Nb is added into microalloyed steel, in the controlled rolling process, a strain-induced precipitated phase can remarkably reduce the recrystallization temperature of deformed austenite through the action of mass point pinning and a subgrain boundary, provide nucleation mass points and have obvious effect on refining grains; in the continuous annealing austenitizing process, carbon and nitride which are not dissolved in the soaking process can prevent the soaking austenite grains from coarsening through a mass point pinning grain boundary mechanism, so that the grains are effectively refined. Therefore, the mass percent of Nb in the cold-rolled annealed dual-phase steel is controlled to be 0.01-0.03%.
In some preferred embodiments, the mass percentage of Nb can be controlled between 0.015 and 0.025%.
Ti: in the cold-rolled annealed dual-phase steel according to the present invention, the added strong carbide-forming element Ti also exhibits a strong effect of suppressing the growth of austenite grains at high temperatures, and the addition of Ti contributes to the refinement of grains. Therefore, the mass percent of Ti in the cold-rolled annealed dual-phase steel is controlled to be 0.01-0.03%.
In some preferred embodiments, the mass percentage of Ti can be controlled between 0.015 and 0.025%.
In the above composition design, the cold-rolled annealed dual-phase steel is not added with precious alloy elements such as Mo, Cr and the like to ensure economy, and meanwhile, in order to ensure that tensile strength of 780MPa grade is obtained at normal continuous annealing gas cooling speed of 40-100 ℃/s, the composition needs to ensure C, Mn alloy addition content to provide sufficient hardenability. However, the content of C, Mn alloy element needs to be controlled by an upper limit to ensure excellent welding performance and formability and avoid the strength exceeding the upper limit.
Due to the competitive precipitation relationship of Al nitride and Nb and Ti carbonitride in the steel production process, the addition of Nb and Ti can play a role in refining grains only by ensuring certain amount by combining the Al and N contents in the component system of the invention. Therefore, the mass percentage content of Nb and Ti in the cold-rolled annealed dual-phase steel can also accord with the formula: nb% + Ti% × 3 is not less than 0.047%. In the formula, Nb and Ti both represent the mass percentage content of the corresponding elements, namely the numerical value in the formula before the percentage number.
Further, in the cold-rolled annealed dual-phase steel of the present invention, the chemical elements thereof are contained in mass% so as to satisfy at least one of the following:
C：0.11％～0.125％，
Si：0.5％～0.7％，
Mn：1.7％～1.8％，
Al：0.015％～0.045％，
Nb：0.015～0.025％，
Ti：0.015～0.025％。
further, in the cold-rolled annealed dual-phase steel according to the present invention, the inevitable impurities include P, S and N elements, and the content thereof is controlled to be at least one of: p is less than or equal to 0.015 percent, S is less than or equal to 0.003 percent, and N is less than or equal to 0.005 percent.
In the above technical solution, P, N and S are inevitable impurity elements in the cold-rolled annealed dual phase steel of the present invention, and the lower the contents of P, N and S elements in the steel, the better the implementation effect. MnS formed by S seriously influences the forming performance, and N easily causes cracks or bubbles on the surface of a plate blank. Therefore, in the cold-rolled annealed dual-phase steel, the mass percent of P is controlled to be less than or equal to 0.015 percent, the mass percent of S is controlled to be less than or equal to 0.003 percent, and the mass percent of N is controlled to be less than or equal to 0.005 percent.
Further, in the cold-rolled annealed dual-phase steel according to the present invention, the phase ratio of martensite is > 55%.
Further, in the cold-rolled annealed dual-phase steel according to the present invention, the grain diameter of the martensite is not more than 5 μm, and the grain diameter of the ferrite is not more than 5 μm.
Further, in the cold-rolled annealed dual-phase steel of the present invention, the properties satisfy at least one of the following: the yield strength is more than or equal to 420 MPa; the tensile strength is more than 780 MPa; a. the50The gauge length fracture elongation is more than or equal to 18 percent; the 90-degree cold bending performance characterization parameter R/t is less than or equal to 1, wherein R represents the bending radius, t represents the plate thickness, and the unit parameter is mm.
Accordingly, another object of the present invention is to provide a method for manufacturing a cold-rolled annealed dual-phase steel having characteristics of high strength, excellent elongation and cold bending properties, a yield strength of not less than 420MPa, a tensile strength of greater than 780MPa, and A50The gauge length fracture elongation is more than or equal to 18 percent, and the 90-degree cold bending performance characterization parameter R/t is less than or equal to 1, wherein R represents the bending radius, t represents the plate thickness, and the unit parameter is mm.
In order to achieve the above object, the present invention provides the above method for manufacturing cold-rolled annealed dual-phase steel, comprising the steps of:
(1) smelting and continuous casting;
(2) hot rolling;
(3) cold rolling;
(4) annealing: the annealing soaking temperature is 770-820 ℃, the annealing time is 40-200 s, then the steel is cooled to the rapid cooling starting temperature at the speed of 3-5 ℃/s, and then the steel is rapidly cooled at the speed of 30-80 ℃/s, wherein the rapid cooling starting temperature is 650-730 ℃, and the rapid cooling ending temperature is 200-270 ℃;
(5) tempering;
(6) and (7) flattening.
In the method for manufacturing the cold-rolled annealed dual-phase steel, in the step (4), the annealing soaking temperature is controlled to be 770-820 ℃ because: when the annealing soaking temperature is lower than 790 ℃, the steel with 780MPa tensile strength cannot be obtained; if the annealing soaking temperature is higher than 820 ℃, the grain size is large, and the formability is greatly reduced. Therefore, the tensile strength of 780MPa can be ensured by controlling the annealing soaking temperature to be 770-820 ℃, and the obtained crystal grain size is small, so that the cold-rolled annealed dual-phase steel has better forming performance.
In some preferred embodiments, in order to obtain better implementation effect, the obtained crystal grain size is finer, the obtained steel has moderate mechanical property and better forming performance, and the annealing soaking temperature can be controlled between 790 ℃ and 810 ℃.
Further, in the manufacturing method of the invention, in the step (2), the slab is heated to 1160-; controlling the coiling temperature to be 500-600 ℃, and cooling in air after coiling.
Further, in the manufacturing method of the present invention, in the step (3), the cold rolling reduction is controlled to be 50 to 70%.
Further, in the manufacturing method of the present invention, in the step (5), the tempering temperature is controlled to be 200-.
Further, in the manufacturing method of the present invention, in the step (6), the flattening reduction rate is controlled to be not more than 0.3%.
Further, in the manufacturing method of the invention, in the step (4), the annealing soaking temperature is 790-810 ℃.
Compared with the prior art, the cold-rolled annealed dual-phase steel and the manufacturing method thereof have the advantages and beneficial effects as follows:
the cold-rolled annealed dual-phase steel adopts reasonable alloy chemical composition design, and obtains a steel plate with a martensite + ferrite dual-phase structure with the tensile strength of more than 780MPa on the premise of not adding Mo and Cr, wherein the yield strength is more than or equal to 420MPa, the tensile strength is more than 780MPa, and A is50The gauge length fracture elongation is more than or equal to 18 percent, and the 90-degree cold bending performance characterization parameterR/t is less than or equal to 1. The characteristics of high strength and excellent elongation and cold bending properties are achieved while having good economy.
Correspondingly, the manufacturing method disclosed by the invention has the advantages that the specific process parameters are reasonably designed and controlled, so that the cold-rolled annealed dual-phase steel obtained by the manufacturing method disclosed by the invention not only has good economical efficiency, but also has the characteristics of high strength and excellent elongation and cold bending performance.
Detailed Description
The economical 780MPa grade cold-rolled annealed dual-phase steel and the method for manufacturing the same according to the present invention will be further explained and illustrated with reference to the following specific examples, which, however, should not be construed to unduly limit the technical scope of the present invention.
Examples 1 to 7 and comparative examples 1 to 14
Table 1 shows the mass percentages of the chemical elements in the steel grades corresponding to the cold-rolled annealed dual-phase steels of examples 1 to 7 and the steels of comparative examples 1 to 14.
Table 1 (wt%, balance Fe and other unavoidable impurities except P, S and N)
The cold-rolled annealed dual-phase steels of examples 1 to 7 according to the present invention and the steels of comparative examples 1 to 14 were prepared by the following steps:
(1) smelting and continuous casting: obtaining required alloy components, and reducing the content of S, P as much as possible;
(2) hot rolling: heating the plate blank to 1160-; controlling the coiling temperature to be 500-600 ℃, and cooling in air after coiling;
(3) cold rolling: controlling the cold rolling reduction rate to be 50-70%;
(4) annealing: the annealing soaking temperature is controlled to be 770-820 ℃, and can also be preferably controlled to be 790-810 ℃, the annealing time is controlled to be 40-200 s, then the annealing is cooled to the rapid cooling starting temperature at the speed of 3-5 ℃/s, and then the annealing is rapidly cooled at the speed of 30-80 ℃/s, wherein the rapid cooling starting temperature is 650-730 ℃, and the rapid cooling ending temperature is 200-270 ℃;
(5) tempering: the annealing temperature is controlled to be 200-270 ℃, and the annealing time is controlled to be 100-400 s.
(6) Leveling: the leveling reduction rate is controlled to be less than or equal to 0.3 percent.
It is to be noted that the chemical compositions and the relevant process parameters of the cold rolled annealed dual phase steels of examples 1-7 all meet the design specification control requirements of the present invention. The steel chemical compositions of comparative examples 1 to 6 all have parameters that do not satisfy the requirements of the design of the present invention; the chemical compositions of the N steel grades corresponding to the comparative examples 7-14 meet the design requirements of the invention, but related process parameters have parameters which can not meet the design specifications of the invention.
Tables 2-1 and 2-2 list specific process parameters for the cold rolled annealed dual phase steels of examples 1-7 and the steels of comparative examples 1-14.
Table 2-1.
Table 2-2.
It should be noted that, as shown in table 2-2, the rapid cooling end temperature and the tempering temperature of each of the examples and comparative examples were the same because the tempering operation was performed immediately after the rapid cooling operation was ended during the actual process operation.
The cold-rolled annealed dual-phase steels of examples 1 to 7 and the steels of comparative examples 1 to 14 were subjected to various performance tests, and the test results obtained are shown in Table 3.
Table 3 shows the results of the performance tests of the cold-rolled annealed dual-phase steels of examples 1 to 7 and the steels of comparative examples 1 to 14.
Table 3.
As can be seen from Table 3, examples 1-7 which meet the design specification control requirements of the present invention are excellent in performance, and the yield strengths thereof are all equal to or greater than 420 MPa; the tensile strength is greater than 780MPa, A50The gauge length fracture elongation is more than or equal to 18 percent, and the 90-degree cold bending performance characterization parameter R/t is less than or equal to 1(R represents the bending radius, t represents the plate thickness, and the unit parameter is mm). The cold-rolled annealed dual-phase steel of each embodiment has excellent performance, obtains tensile strength more than 780MPa on the premise of not adding noble alloy elements such as Mo, Cr and the like, and has good elongation and excellent cold bending performance.
It should be noted that the prior art in the protection scope of the present invention is not limited to the examples given in the present application, and all the prior art which is not inconsistent with the technical scheme of the present invention, including but not limited to the prior patent documents, the prior publications and the like, can be included in the protection scope of the present invention. In addition, the combination of the features in the present application is not limited to the combination described in the claims of the present application or the combination described in the embodiments, and all the features described in the present application may be freely combined or combined in any manner unless contradictory to each other.
It should also be noted that the above-mentioned embodiments are only specific embodiments of the present invention. It is apparent that the present invention is not limited to the above embodiments and similar changes or modifications can be easily made by those skilled in the art from the disclosure of the present invention and shall fall within the scope of the present invention.
Claims (14)
1. The economical 780 MPa-grade cold-rolled annealed dual-phase steel is characterized in that the matrix structure is fine and uniform martensite + ferrite, and the cold-rolled annealed dual-phase steel contains the following chemical elements in percentage by mass besides Fe:
C：0.1％～0.13％，Si：0.4％～0.8％，Mn：1.65％～1.9％，Al：0.01％～0.05％，Nb：0.01～0.03％，Ti：0.01～0.03％；
and the cold-rolled annealed dual-phase steel does not contain Cr and Mo elements.
2. The cold-rolled annealed dual-phase steel according to claim 1, wherein the chemical elements are, in mass percent:
c: 0.1% -0.13%, Si: 0.4-0.8%, Mn: 1.65% -1.9%, Al: 0.01 to 0.05 percent, Nb: 0.01-0.03%, Ti: 0.01-0.03%, and the balance of Fe and other inevitable impurities.
3. The cold-rolled annealed dual-phase steel according to claim 1 or 2, characterized in that the content of each chemical element by mass satisfies at least one of the following:
C：0.11％～0.125％，
Si：0.5％～0.7％，
Mn：1.7％～1.8％，
Al：0.015％～0.045％，
Nb：0.015～0.025％，
Ti：0.015～0.025％。
4. the cold-rolled annealed dual-phase steel as set forth in claim 2, wherein the inevitable impurities include P, S and N elements, the contents of which are controlled to be at least one of: p is less than or equal to 0.015 percent, S is less than or equal to 0.003 percent, and N is less than or equal to 0.005 percent.
5. The cold-rolled annealed dual-phase steel according to claim 1 or 2, wherein the contents of Nb and Ti in mass% further satisfy: nb% + Ti% × 3 is not less than 0.047%.
6. Cold-rolled annealed dual-phase steel according to claim 1 or 2, characterised in that the phase proportion of martensite is > 55%.
7. The cold-rolled annealed dual-phase steel as set forth in claim 1 or 2, wherein said martensite has a grain diameter of not more than 5 μm, and said ferrite has a grain diameter of not more than 5 μm.
8. The cold-rolled annealed dual-phase steel according to claim 1 or 2, characterized in that its properties satisfy at least one of the following: the yield strength is more than or equal to 420 MPa; the tensile strength is more than 780 MPa; a. the50The gauge length fracture elongation is more than or equal to 18 percent; the 90-degree cold bending performance characterization parameter R/t is less than or equal to 1, wherein R represents the bending radius, t represents the plate thickness, and the unit parameter is mm.
9. A method of manufacturing a cold-rolled annealed dual-phase steel according to any one of claims 1 to 8, characterized by comprising the steps of:
(1) smelting and continuous casting;
(2) hot rolling;
(3) cold rolling;
(4) annealing: the annealing soaking temperature is 770-820 ℃, the annealing time is 40-200 s, then the steel is cooled to the rapid cooling starting temperature at the speed of 3-5 ℃/s, and then the steel is rapidly cooled at the speed of 30-80 ℃/s, wherein the rapid cooling starting temperature is 650-730 ℃, and the rapid cooling ending temperature is 200-270 ℃;
(5) tempering;
(6) and (7) flattening.
10. The manufacturing method as claimed in claim 9, wherein in the step (2), the slab is heated to 1160-; controlling the coiling temperature to be 500-600 ℃, and cooling in air after coiling.
11. The manufacturing method according to claim 9, wherein in the step (3), the cold rolling reduction is controlled to be 50 to 70%.
12. The method as claimed in claim 9, wherein in the step (5), the annealing temperature is controlled to be 200 ℃ and the annealing time is controlled to be 100 ℃ and 400 seconds.
13. The production method according to claim 9, wherein in the step (6), the flattening reduction is controlled to 0.3% or less.
14. The method according to any one of claims 9 to 13, wherein in step (4), the annealing soaking temperature is 790-810 ℃.
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| CN202010459214.0A CN113737086A (en) | 2020-05-27 | 2020-05-27 | Economical 780 MPa-grade cold-rolled annealed dual-phase steel and manufacturing method thereof |
| US17/927,875 US20230203611A1 (en) | 2020-05-27 | 2021-05-25 | 780 mpa-class cold-rolled and annealed dual-phase steel and manufacturing method therefor |
| PCT/CN2021/095808 WO2021238917A1 (en) | 2020-05-27 | 2021-05-25 | 780 mpa-class cold-rolled and annealed dual-phase steel and manufacturing method therefor |
| CA3180469A CA3180469A1 (en) | 2020-05-27 | 2021-05-25 | 780 mpa-class cold-rolled and annealed dual-phase steel and manufacturing method therefor |
| JP2022572703A JP7524357B2 (en) | 2020-05-27 | 2021-05-25 | 780MPa-class cold-rolled annealed dual-phase steel and its manufacturing method |
| EP21813104.3A EP4159885A4 (en) | 2020-05-27 | 2021-05-25 | 780 mpa-class cold-rolled and annealed dual-phase steel and manufacturing method therefor |
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| JP7524357B2 (en) | 2024-07-29 |
| CA3180469A1 (en) | 2021-12-02 |
| JP2023527390A (en) | 2023-06-28 |
| EP4159885A4 (en) | 2024-04-24 |
| US20230203611A1 (en) | 2023-06-29 |
| EP4159885A1 (en) | 2023-04-05 |
| WO2021238917A1 (en) | 2021-12-02 |
| EP4159885A9 (en) | 2023-06-21 |
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Application publication date: 20211203 |