CN115927959B - 2.2 GPa-grade low-cost low-carbon heterogeneous lamellar ultra-high-strength dual-phase steel and preparation method thereof - Google Patents
2.2 GPa-grade low-cost low-carbon heterogeneous lamellar ultra-high-strength dual-phase steel and preparation method thereof Download PDFInfo
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Abstract
The invention discloses 2.2 GPa-level low-cost low-carbon heterogeneous lamellar ultra-high-strength dual-phase steel and a preparation method thereof, and belongs to the field of metal materials. The dual-phase steel comprises the following chemical components in percentage by mass (wt.%) of alloy elements: 0.10 to 0.15, mn:1.10 to 1.80, si:1.10 to 1.35, al:0.30 to 0.45, (Ti+V+Zr) is less than 0.1, S is less than or equal to 0.008, P is less than or equal to 0.015, and the balance is Fe and other unavoidable impurities; the preparation method adopts a vacuum furnace smelting, an austenite region rolling process for rolling, water quenching is directly carried out after rolling and cooling to room temperature, then cyclic heat treatment is carried out in a KSL-1100X heating furnace to obtain high-strength high-plasticity lamellar dual-phase steel, and finally 80% -85% high-pressure warm rolling is carried out at 250 ℃ -350 ℃ to obtain the ultra-high-strength dual-phase steel with low cost, tensile strength of more than or equal to 2.2GPa, yield strength of more than or equal to 1.8GPa and elongation after breaking of more than or equal to 5%.
Description
Technical Field
The invention relates to the field of production and preparation of dual-phase steel, in particular to 2.2 GPa-level low-carbon low-cost lamellar interphase martensite-ferrite ultra-high strength heterogeneous dual-phase steel and a preparation method thereof.
Background
The weight reduction of various structural materials is one of the effective means for realizing the reduction of carbon emissions, and ultra-high strength steels of the order of 2.0GPa and above are the future development direction of the weight-reduced structural materials.
In terms of development of the existing ultra-high strength steel, the ultra-high strength steel can be divided into three directions, wherein the first direction is low alloy ultra-high strength steel, the ultra-high strength steel is mainly characterized in that carbon is controlled to be 0.3% -0.5%, and then alloy elements with higher prices such as Mo, ni, cr and V are added for strengthening, so that the yield strength can be ensured to be more than 1300 MPa; the second direction is secondary hardening ultra-high strength steel, which is commonly added with expensive elements of Cr, ni, mo and Co, and is subjected to secondary hardening by quenching and high-temperature tempering, so that ultra-high strength can be realized; in the third direction, the ultra-high strength maraging steel is obtained by adding metals such as Mo, ti, co and the like into an Fe-Ni martensitic alloy, and precipitating nano-scale intermetallic compounds through aging, so that the strength is greatly improved. Although the above composition design and treatment means can produce ultra-high strength steel, the material cost is in a high or extremely high range. Therefore, the ultra-high strength steel has low cost and excellent competitive advantage
At present, researches on ultra-high strength steel of 2.0GPa and above mainly aim at medium carbon hot forming steel and high alloy aging steel, and patent CN 106811689A discloses hot forming steel with tensile strength larger than 2.0GPa, which is prepared by mainly performing cold rolling on a hot rolled steel plate by more than 70%, and then performing quenching treatment on an annealed sample to finally obtain hot forming steel with tensile strength larger than 2.0GPa; the patent CN 112267067A discloses a hot rolled steel plate for a 2.0 GPa-grade hot stamping wheel rim, and the main process is that the hot rolled steel plate is subjected to pre-deformation of more than 70 percent and then is subjected to stamping forming, so that the ultra-high strength steel with the tensile strength of more than 2.0GPa and the yield strength of more than 1.5GPa is finally obtained; the patent CN 113198928A discloses a hot stamping formed part with the strength of 2.0GPa and the strength-plastic product of 20 GPa percent and a manufacturing method thereof, wherein the quenching property and carbide stability of the material are mainly improved by Cr element, and then the annealed cold-rolled plate is subjected to hot stamping forming, so that the strength of a finished product can reach 2.0GPa; patent CN 114517267A discloses an ultra-low carbon high performance maraging stainless steel, in which mainly a large amount of expensive metal is added, and a martensitic steel with a tensile strength exceeding 2.0GPa is obtained by an aging process.
On the basis of many researches on ultra-high strength steel, the invention develops the 0.15C, low alloy component and noble metal-free warm rolling 2.2 GPa-grade low-cost low-carbon heterogeneous lamellar ultra-high strength dual-phase steel for further reducing the material cost and the carbon content on the basis of ultra-high strength.
Disclosure of Invention
The invention discloses a martensite-ferrite super-strength dual-phase steel formed by alternately arranging lamellar martensite and ferrite through a warm rolling process of controlling the morphology of martensite and ferrite tissues in the martensite-ferrite dual-phase steel and then carrying out large deformation. The tensile strength of the low-carbon low-cost ultrahigh-strength steel can reach 2.2GPa, the elongation after fracture is more than or equal to 5 percent, the ultra-high strength is ensured, and meanwhile, the ultra-low cost advantage of only 0.15C and low alloy content is achieved. The invention well solves the problems of higher carbon content, more alloy components, high price and the like of the ultra-high strength structural steel.
In order to solve the technical problems, the invention provides the following technical scheme:
2.2 GPa-grade low-cost low-carbon lamellar ultra-high strength dual-phase steel comprises the following chemical components: 0.10 to 0.15, mn:1.10 to 1.80, si:1.10 to 1.35, al:0.30 to 0.45, (Ti+V+Zr) < 0.1, S is less than or equal to 0.008, P is less than or equal to 0.015, and the balance is Fe and other unavoidable impurities.
A preparation method of 2.2GPa grade low-cost low-carbon heterogeneous lamellar ultra-high-strength dual-phase steel can produce the 2.2GPa grade lamellar interphase martensite-ferrite ultra-high-strength heterogeneous dual-phase steel by reasonably controlling the heat preservation temperature, the heat preservation time and the rolling temperature in a given range. The preparation method comprises the following steps:
(1) Smelting and forging: smelting in a vacuum induction furnace, accurately controlling alloy components and strictly controlling P, S and element contents in the process, forging the ingot into square billets in a laboratory after obtaining the ingot, wherein the final forging temperature is higher than 965 ℃;
(2) Heating: heating by a KSL-1200X resistance furnace at 1180-1200 ℃ for 95-118min, and removing iron oxide scale after discharging;
(3) Rolling: rolling the heated blank, wherein the initial rolling temperature is 1030-1090 ℃, and the final rolling temperature is 950-970 ℃ after multi-pass rolling;
(4) And (3) cooling: performing direct water quenching treatment on the rolled steel plate obtained in the step (3);
(5) And (3) heat treatment: and (3) performing heat treatment on the quenched sample obtained in the step (4), heating the sample to a certain temperature in the temperature range of Ac 1-Ac 3, preserving heat for 2-3min, and quenching with water to room temperature, wherein the heat treatment mode is performed repeatedly for 2 times or more, and 3 times are selected.
(6) Placing the heat-treated sample in a KSL-1100X heating furnace at 300-350 ℃, preserving heat for 18-22min, heating a cold rolling mill roller to 300-350 ℃ by using asbestos heated to 500 ℃, then placing the 300-350 ℃ sample into a rolling mill for warm rolling, preserving heat in the heating furnace for 2-4min after each pass of rolling, and finally ensuring the total reduction to be 80-85%, thus obtaining the 2.2 GPa-grade low-cost low-carbon heterogeneous lamellar ultra-high strength dual-phase steel.
The room temperature structure of the dual-phase steel is a dual-phase structure formed by alternately arranging ultra-thin heterogeneous lamellar martensite and ferrite, the lamellar thickness is less than 200nm, the tensile strength is more than or equal to 2.2GPa, the yield strength is more than or equal to 1.8GPa, and the elongation after forging is more than or equal to 5%.
The invention provides a low-carbon, low-cost and 2.2 GPa-grade lamellar interphase martensite-ferrite constituted ultra-high strength dual-phase steel and a preparation method thereof, wherein the chemical components and the alloy element mass percentage (wt%) contents thereof are C:0.10 to 0.15, mn:1.10 to 1.80, si:1.10 to 1.35, al:0.30 to 0.45, (Ti+V+Zr) < 0.1, S is less than or equal to 0.008, P is less than or equal to 0.015, and the balance is Fe and other unavoidable impurities. The mechanical property is that the tensile strength is more than or equal to 2.2GPa, the yield strength is more than or equal to 1.8GPa, and the elongation after breaking is more than or equal to 5%; the room temperature structure is a two-phase structure formed by alternately arranging ultrathin lamellar martensite and ferrite.
The invention also provides a specific preparation method of the ultra-high strength steel, the product is smelted by adopting a vacuum furnace, the content of harmful elements such as P, S is strictly controlled, 25kg of cast ingot is obtained, and then 70mm multiplied by 70mm forging stock is formed in a laboratory, and the specific rolling process is as follows: heating the forging stock to 1180-1200 deg.c in a heating furnace, maintaining for 95-118min, taking out to eliminate surface iron scale, rolling in a laboratory mill at 1030-1090 deg.c, multipass rolling in austenitic region at 950-970 deg.c, direct water quenching to room temperature, setting at 900 deg.c for 2-3min, direct quenching to room temperature, repeating the heat treatment for 2 times or more, final warm rolling at 350 deg.c to total rolling reduction of 80-85%, and final obtaining the 2.2GPa low carbon low cost superhigh strength heterogeneous double phase steel.
The technical key points of the invention are as follows:
the invention adopts low-carbon design, the alloy element has low price, a small amount of micro alloy element has great advantages in low carbon and low cost, and typical alloy components and percentage contents of the invention and the comparative steel are shown in table 1.
Table 1 comparison of the alloy compositions of the present invention with typical compositions of the comparative invention (wt.%)
The invention has the main advantages compared with the prior invention that the following 3 points are:
(1) Compared with the traditional ultra-high strength steel design, the invention does not use a large amount of expensive alloy elements in component design, and has great advantages in cost control;
(2) In the production process, the method adopts the process of directly quenching after rolling and combining the two-phase region with short-time heat-preserving quenching and then carrying out simple warm rolling, so that the product has high stability and mass production potential;
(3) The product structure of the invention is mainly formed by alternating arrangement of lamellar martensite and lamellar ferrite, and the microstructure of the martensite-ferrite lamellar phase can ensure that the tensile strength is more than 2.2GPa, and meanwhile, the C content of the invention is only 0.15, which is far lower than the level of the similar strength ultra-high strength steel, and has great advantages in welding performance.
Description of the attached tables
Table 1 shows the design composition of the invention compared with the composition of the comparative steel grade alloy;
table 2 shows the chemical compositions and the mass percentages of alloy elements corresponding to the steel types in the embodiment of the invention;
table 3 shows the mechanical property data of the examples of the invention.
Drawings
FIG. 1 is an SEM image of the 2.2GPa grade low-cost low-carbon heterogeneous lamellar ultra-high dual phase steel corresponding to example 1;
FIG. 2 is an SEM image of the 2.2 GPa-grade low-cost low-carbon heterogeneous lamellar ultra-high-strength dual-phase steel corresponding to example 2;
fig. 3 is an SEM image of the 2.2GPa grade low-cost, low-carbon heterogeneous lamellar ultra-high-strength dual-phase steel corresponding to example 3.
Detailed Description
The following examples are given to further illustrate the technical aspects of the present invention, but are not limited thereto.
The embodiment is 2.2 GPa-level low-cost low-carbon heterogeneous lamellar ultra-high-strength dual-phase steel, which is characterized in that the chemical components of the dual-phase steel are C:0.10 to 0.15, mn:1.10 to 1.80, si:1.10 to 1.35, al:0.30 to 0.45, (Ti+V+Zr) is less than 0.1, S is less than or equal to 0.008, P is less than or equal to 0.015, and the balance is Fe and other unavoidable impurities; the specific chemical compositions and the percentage (wt.%) of the alloy elements are shown in table 2.
Table 2 chemical composition (wt.%) of the examples of the invention
Example 1
The embodiment produces 2.2 GPa-grade low-cost low-carbon heterogeneous lamellar ultra-high-strength dual-phase steel, and the specific production process of the ultra-high-strength dual-phase steel comprises the following steps: placing the forging stock in a heating furnace with the set temperature of 1180 ℃, preserving heat for 125min, taking out the steel billet after heat preservation to remove oxidized iron scales, rolling the steel billet into a steel plate with 8mm in an austenite region through multi-pass rolling, wherein the initial rolling temperature is 1080 ℃, the final rolling temperature is 970 ℃, then directly quenching the steel plate to room temperature by water, placing the steel plate in a KSL-1100X heating furnace with the temperature of 900 ℃ between Ac1 and Ac3, preserving heat for 3min after the temperature is constant, directly quenching the steel plate to room temperature by water, circularly repeating the operation for 3 times in a heat treatment mode, and then carrying out warm rolling on the sample at the temperature of 350 ℃ to obtain the ultra-high strength dual-phase steel with the final thickness of 1.5mm, wherein the tensile strength is 2.238GPa, the yield strength is 1.983GPa and the elongation is 5.3%.
Example 2
The embodiment produces 2.2 GPa-grade low-cost low-carbon heterogeneous lamellar ultra-high-strength dual-phase steel, and the specific production process of the ultra-high-strength dual-phase steel comprises the following steps: placing the forging stock in a heating furnace with the set temperature of 1180 ℃, preserving heat for 125min, taking out the steel billet after heat preservation to remove oxidized iron scales, rolling the steel billet into a steel plate with the thickness of 1.6mm after multi-pass rolling in an austenite region, wherein the initial rolling temperature is 1090 ℃ and the final rolling temperature is 960 ℃ in the rolling process, then directly quenching the steel plate to room temperature, placing the steel plate in a KSL-1100X heating furnace with the temperature of 900 ℃ between Ac1 and Ac3, preserving heat for 3min after the temperature is constant, directly quenching the steel plate to room temperature, circularly repeating the operation for 3 times in a heat treatment mode, and then carrying out warm rolling on the steel plate at the temperature of 330 ℃ to obtain the ultra-high strength dual-phase steel with the final thickness of 1.6mm, wherein the tensile strength is 2.224GPa, the yield strength is 2.015GPa and the elongation is 5.5%.
Example 3
The embodiment produces 2.2 GPa-grade low-cost low-carbon heterogeneous lamellar ultra-high-strength dual-phase steel, and the specific production process of the ultra-high-strength dual-phase steel comprises the following steps: placing the forging stock in a heating furnace with the set temperature of 1180 ℃, preserving heat for 125min, taking out the steel billet after heat preservation to remove oxidized iron scales, rolling the steel billet into a steel plate with the thickness of 1.4mm in an austenite region through multi-pass rolling, wherein the initial rolling temperature is 1090 ℃ and the final rolling temperature is 970 ℃ in the rolling process, then directly quenching the steel plate to room temperature, placing the steel plate in a KSL-1100X heating furnace with the temperature of 900 ℃ between Ac1 and Ac3, preserving heat for 3min after the temperature is constant, directly quenching the steel plate to room temperature, circularly repeating the operation for 3 times in a heat treatment mode, and then carrying out warm rolling on the steel plate at the temperature of 320 ℃ to obtain the ultra-high strength dual-phase steel with the final thickness of 1.4mm, wherein the tensile strength is 2.215GPa, the yield strength is 1.992GPa and the elongation is 5.8%.
Table 3 shows the mechanical properties data corresponding to the three examples
| Examples reference numerals | YS/GPa | UTS/GPa | EL/％ |
| Example 1 | 1.983 | 2.238 | 5.3 |
| Example 2 | 2.015 | 2.224 | 5.5 |
| Example 3 | 1.992 | 2.215 | 5.8 |
Claims (2)
1. The 2.2 GPa-grade low-cost low-carbon heterogeneous lamellar ultra-high-strength dual-phase steel is characterized by comprising the following chemical components in percentage by mass: 0.10-0.15, mn: 1.10-1.80, si: 1.10-1.35, al: 0.30-0.45, (Ti+V+Zr) < 0.1, S less than or equal to 0.008, P less than or equal to 0.015, and the balance of Fe and other unavoidable impurities;
the heat preservation temperature, the heat preservation time and the rolling temperature are reasonably controlled in a given range, so that the martensite-ferrite ultra-high strength dual-phase steel with 2.2GPa grade lamellar interphase can be produced; the preparation method comprises the following steps:
(1) Smelting and forging: smelting in a vacuum induction furnace, accurately controlling alloy components and strictly controlling the content of P, S elements in the process, forging the ingot into square billets in a laboratory after obtaining the ingot, wherein the final forging temperature is greater than 965 ℃;
(2) Heating: heating by a KSL-1200X resistance furnace at 1130-1180deg.C for 95-118min, and removing iron oxide scale after discharging;
(3) Rolling: rolling the heated blank, wherein the initial rolling temperature is 1030-1090 ℃, the multi-pass rolling is carried out, and the final rolling temperature is 950-970 ℃;
(4) And (3) cooling: performing direct water quenching treatment on the rolled steel plate obtained in the step (3);
(5) And (3) heat treatment: carrying out heat treatment on the quenched sample obtained in the step (4), heating the sample to a certain temperature within the temperature range of Ac 1-Ac 3, preserving heat for 2-3min, and quenching the sample with water to room temperature, wherein the heat treatment mode is carried out repeatedly for 2 times or more;
(6) Placing the heat-treated sample in a KSL-1100X heating furnace at 300-350 ℃, preserving heat for 18-22min, firstly heating the surface of a cold rolling mill roller to 300-350 ℃ by using asbestos heated to 500 ℃, then placing the 300-350 ℃ sample into a rolling mill for warm rolling, and after each pass of rolling, preserving heat for 2-4min in the heating furnace again, finally ensuring the total reduction to be 80-85%, thus obtaining the 2.2 GPa-grade low-cost low-carbon heterogeneous lamellar ultra-high strength dual-phase steel.
2. The 2.2 GPa-grade low-cost low-carbon heterogeneous lamellar ultra-high-strength dual-phase steel according to claim 1, wherein the room-temperature structure of the dual-phase steel is a dual-phase structure formed by alternately arranging ultra-thin heterogeneous lamellar martensite and ferrite, the lamellar thickness is less than 200nm, the tensile strength is more than or equal to 2.2GPa, the yield strength is more than or equal to 1.8GPa, and the elongation after forging is more than or equal to 5%.
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Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1765568A (en) * | 2005-11-18 | 2006-05-03 | 东北大学 | Method for manufacturing nano-crystal particle low carbon micro alloy steel |
| JP2015151576A (en) * | 2014-02-13 | 2015-08-24 | 新日鐵住金株式会社 | HIGH STRENGTH STEEL SHEET HAVING MAXIMUM TENSILE STRENGTH OF 1300 MPa OR MORE AND EXCELLENT IN MOLDABILITY, HIGH STRENGTH GALVANIZED STEEL SHEET, HIGH STRENGTH ALLOY GALVANIZED STEEL SHEET AND MANUFACTURING METHOD THEREFOR |
| CN108018503A (en) * | 2017-11-28 | 2018-05-11 | 西安交通大学 | A kind of stratiform Ultra-fine Grained dual phase ferritic/martensite steel and preparation method thereof |
| CN110578095A (en) * | 2019-10-22 | 2019-12-17 | 马鞍山钢铁股份有限公司 | 1200 MPa-level hot-rolled ultrahigh-strength steel plate and manufacturing method thereof |
| CN111041376A (en) * | 2020-01-08 | 2020-04-21 | 湖南科技大学 | Preparation method of 2000 MPa-level ultrahigh-strength TRIP steel |
| WO2021032858A1 (en) * | 2019-08-21 | 2021-02-25 | Ilsenburger Grobblech Gmbh | Method for producing high-strength sheets or strips from a low-alloy, high-strength bainitic steel, and steel strip or steel sheet made of said steel |
| CN114293111A (en) * | 2021-12-08 | 2022-04-08 | 北京科技大学 | 1.1 GPa-grade martensite-ferrite dual-phase steel with alternate lamellar layers and preparation method thereof |
| CN114703417A (en) * | 2022-04-11 | 2022-07-05 | 常州大学 | Method for preparing superfine-grain high-toughness medium manganese steel based on TWIP effect and microalloy precipitation |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP5754279B2 (en) * | 2011-07-20 | 2015-07-29 | Ｊｆｅスチール株式会社 | High strength steel sheet for warm forming and manufacturing method thereof |
-
2022
- 2022-11-15 CN CN202211432397.2A patent/CN115927959B/en active Active
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1765568A (en) * | 2005-11-18 | 2006-05-03 | 东北大学 | Method for manufacturing nano-crystal particle low carbon micro alloy steel |
| JP2015151576A (en) * | 2014-02-13 | 2015-08-24 | 新日鐵住金株式会社 | HIGH STRENGTH STEEL SHEET HAVING MAXIMUM TENSILE STRENGTH OF 1300 MPa OR MORE AND EXCELLENT IN MOLDABILITY, HIGH STRENGTH GALVANIZED STEEL SHEET, HIGH STRENGTH ALLOY GALVANIZED STEEL SHEET AND MANUFACTURING METHOD THEREFOR |
| CN108018503A (en) * | 2017-11-28 | 2018-05-11 | 西安交通大学 | A kind of stratiform Ultra-fine Grained dual phase ferritic/martensite steel and preparation method thereof |
| WO2021032858A1 (en) * | 2019-08-21 | 2021-02-25 | Ilsenburger Grobblech Gmbh | Method for producing high-strength sheets or strips from a low-alloy, high-strength bainitic steel, and steel strip or steel sheet made of said steel |
| CN110578095A (en) * | 2019-10-22 | 2019-12-17 | 马鞍山钢铁股份有限公司 | 1200 MPa-level hot-rolled ultrahigh-strength steel plate and manufacturing method thereof |
| CN111041376A (en) * | 2020-01-08 | 2020-04-21 | 湖南科技大学 | Preparation method of 2000 MPa-level ultrahigh-strength TRIP steel |
| CN114293111A (en) * | 2021-12-08 | 2022-04-08 | 北京科技大学 | 1.1 GPa-grade martensite-ferrite dual-phase steel with alternate lamellar layers and preparation method thereof |
| CN114703417A (en) * | 2022-04-11 | 2022-07-05 | 常州大学 | Method for preparing superfine-grain high-toughness medium manganese steel based on TWIP effect and microalloy precipitation |
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