CN112280941A - Preparation method of ultrahigh-strength ductile bainite steel based on stacking fault energy regulation - Google Patents
Preparation method of ultrahigh-strength ductile bainite steel based on stacking fault energy regulation Download PDFInfo
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- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
- C21D1/20—Isothermal quenching, e.g. bainitic hardening
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- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/34—Methods of heating
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
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Abstract
The invention discloses a preparation method of ultra-high-strength ductile bainite steel based on adjustment and control of stacking fault energy, which is characterized in that rolling deformation is carried out for 20-40% at 50-350 ℃ above the critical transition temperature of a steel slippage and twinning deformation mode according to the size of the stacking fault energy of the steel, then 50-80% incomplete bainite phase transformation is carried out in a bainite phase transformation temperature interval, and then 5-20% deformation is carried out in a twinning deformation temperature interval, so that the strength, the plasticity and the toughness of the steel are greatly improved at the same time, and the ultra-high-strength ductile bainite steel is obtained.
Description
Technical Field
The invention relates to a preparation method of ultra-high-strength ductile bainite steel based on stacking fault energy regulation and control, and belongs to the field of steel materials and hot working thereof.
Background
The new generation of steel materials pursues the aims of ultrahigh strength and ultrahigh ductility and toughness, but the traditional manufacturing process method is difficult to simultaneously obtain the effect of improving the strength and the plasticity of the materials, the improvement of the strength of the steel reduces the plasticity of the steel, and the improvement of the plasticity of the steel reduces the strength of the steel. In recent years, materials scientists have conducted a great deal of research and exploration work to achieve exciting research results. Such as: the Lumega plain professor team of Beijing technology university utilizes the second precipitation phase with high density and super coherent to research the maraging steel with the strength of 2.2GPa and the elongation rate of 8.2 percent, and the Huangmingxin professor of hong Kong technology university and the Rohai professor team of Beijing technology university, the designed high-density dislocation D & P steel has the strength of 2.2GPa and the elongation rate of 15 percent. The two provide new design ideas and technical experiences for the development of the ultra-high-strength ductile steel and bring hopes for the engineering application of the ultra-high-strength ductile steel. Meanwhile, a taimen professor team system of the institute of metal of the Chinese academy of sciences reveals the influence rule of the stacking fault energy on the microstructure, the fatigue mechanism and the like of the steel. By optimizing the alloy component design, the group reduces the stacking fault energy to change the micro deformation mode, so that the strength and the plasticity of the steel are improved simultaneously.
Based on the ultrahigh-strength ductile requirement and the theory of regulating and controlling the stacking fault energy of the new generation of materials, the influence of the interaction between the stacking fault and the dislocation and the change of the stacking fault energy on the strengthening and toughening mechanism of the steel is researched, and a new thought can be provided for the chemical components and the design of the manufacturing process of the ultrahigh-strength ductile material.
Disclosure of Invention
The invention provides a preparation method of ultra-high-strength ductile bainite steel based on stacking fault energy regulation. Based on the theory of adjustment and control of the stacking fault energy, the steel in a high-temperature austenitizing state is cooled to be 50-350 ℃ above the critical temperature of a twinning and sliding deformation mode corresponding to the stacking fault energy for 20-40% rolling deformation, so that the storage dislocation density of the steel is increased to improve the strength of a matrix, 50-80% incomplete bainite phase transformation is performed isothermally in a bainite phase transformation temperature interval of the steel, and then 5-20% deformation is performed in a twinning transformation temperature interval corresponding to the stacking fault energy, so that a face-centered cubic structure phase in the matrix forms a twin crystal, and the strength, the plasticity and the toughness of the steel are greatly improved at the same time.
The technical scheme of the invention is as follows:
a super-high-strength ductile carbide-free bainite steel based on stacking fault energy regulation is designed according to the following concept:
1. the steel stacking fault energy regulates and controls the deformation mechanism of the face-centered cubic structure phase, thereby influencing the mechanical properties of the steel: the size of the layer fault value of the steel determines that twin crystal transformation, martensite transformation or dislocation slippage occurs when the face-centered cubic structure phase is stressed, and different deformation mechanisms enable the steel to have different mechanical properties.
2. The magnitude of the stacking fault energy of the steel can be obtained by the following several ways: the method comprises the steps of calculating a G.B.Olson thermodynamic model according to the stacking fault energy, wherein the stacking fault energy of a face-centered cubic structure phase can be regarded as the free energy difference between a face-centered cubic structure and a close-packed hexagonal structure; according to the technical scheme of Reed, the microscopic stress is measured by XRD, and the stacking fault energy is calculated; and thirdly, measuring the stacking fault energy according to the TEM.
3. And testing the bainite transformation dynamics of the steel by using an dilatometer or thermal simulation equipment to obtain the time required by 50-80% of incomplete bainite transformation of the steel at different temperatures in the bainite transformation temperature interval.
4. The core technology is that after the original steel is subjected to solution treatment, rolling deformation is carried out for 20-40% at the temperature 50-350 ℃ above the critical temperature of a slippage and twinning deformation mode corresponding to the stacking fault energy, the dislocation density is increased, then incomplete bainite phase transformation is carried out for 50-80% in a bainite phase transformation temperature range of the steel in an isothermal mode, then deformation is carried out for 5-20% in a twinning deformation temperature range corresponding to the stacking fault energy, a certain number of twin crystals are formed in the residual austenite, and meanwhile, the strength and the plasticity of a matrix are greatly improved.
The preparation process of the ultra-high-ductility carbide-free bainite steel comprises the following steps:
a preparation method of ultrahigh-strength ductile bainite steel based on stacking fault energy regulation comprises the following steps:
firstly, determining the fault energy of steel through testing or calculation, and determining a sliding deformation temperature interval and a twinning deformation temperature interval of the steel corresponding to the fault energy;
forging the steel, cooling to room temperature, heating to 900-1000 ℃, keeping the temperature for 20-60 min, carrying out austenitizing treatment, and then carrying out 20-40% deformation at 50-350 ℃ above the critical transformation temperature of the steel in which sliding deformation and twinning deformation are alternated;
and carrying out isothermal treatment in a bainite transformation temperature interval of the steel, so that after 50-80% of incomplete bainite transformation of the steel occurs, 5-20% of deformation is carried out in the twinning deformation temperature interval of the steel.
Further, in a preferred embodiment of the present invention, the isothermal treatment is performed in a bainite transformation temperature interval of the steel for a time t, which is determined by testing bainite transformation kinetics of the steel and according to a time required for 50 to 80% incomplete bainite transformation of the steel at different temperatures in the bainite transformation temperature interval.
Further, in a preferred embodiment of the present invention, a temperature range in which 5 to 20% deformation is performed after 50 to 80% of incomplete bainite transformation of the steel is performed is a twinning transformation temperature range corresponding to the stacking fault energy.
Further, in the preferred embodiment of the present invention, the chemical composition range of the main elements in the steel is: 0.3-0.7 wt% of C and 1.5-2.5 wt% of Si, and the steel contains one or more of Mn, Cr, Ni, Mo and Al alloy elements.
Further, in a preferred embodiment of the invention, an electric furnace is used for smelting steel ingots, the steel ingots are forged and then cooled to room temperature, and then the steel ingots are heated to 900-1000 ℃ and kept warm for 20-60 min for austenitizing treatment.
Further, in a preferred embodiment of the present invention, the ultra high ductility and toughness bainitic steel contains 10 to 30% by volume of residual austenite.
The invention has the technical advantages that:
1. the application range is wide: the design idea based on the stacking fault energy regulation theory has wide application range and can be applied to medium-high carbon carbide-free bainite steel.
2. The application value is high: the steel prepared based on the theory of regulating and controlling the stacking fault energy has the advantages that the strong plasticity and toughness are greatly improved, and the engineering value is important.
3. The production cost is low: the design idea based on the theory of regulating and controlling the stacking fault energy does not need to add noble metal elements, only changes the process and has low production cost.
Detailed Description
Embodiments of the present invention will be described in detail below with reference to examples, but it will be understood by those skilled in the art that the following examples are only illustrative of the present invention and should not be construed as limiting the scope of the present invention. The examples, in which specific conditions are not specified, were conducted under conventional conditions or conditions recommended by the manufacturer. The reagents or instruments used are not indicated by the manufacturer, and are all conventional products available commercially.
Example 1:
a medium-carbon low-alloy carbide-free bainite steel comprises the following chemical components in percentage by weight: c: 0.49, Si: 1.55, Mn: 1.82, Cr: 1.20, Mo: 0.20, Al: 0.69, and the balance of Fe and a small amount of impurity elements. Tests show that the critical temperature of the composition steel for alternating twinning deformation and slip deformation is 300 ℃; the steel has 70% isothermal bainite transformation within 2h at 240 ℃. The specific process comprises the following steps: smelting the steel ingot with the components in an electric arc furnace, and then heating the steel ingot to 1200 ℃ for forging, wherein the finish forging temperature is not lower than 850 ℃. Austenitizing the steel at 920 ℃ for 30 minutes, controlling the temperature to be cooled to 550 ℃, carrying out hot rolling for 20 percent, rapidly placing the steel in a salt bath furnace at 240 ℃ for 2 hours, carrying out 20 percent rolling deformation, and finally carrying out air cooling to room temperature.
The results of the drawing of the carbide-free bainitic steels treated by this process and the carbide-free bainitic steels austenitized at 920 ℃ for 30 minutes and then austempered at 240 ℃ are shown in table 1. It can be seen that the strength, elongation and toughness of the carbide-free bainite steel processed by the process method are respectively improved by 46%, 8% and 26% compared with the strength, elongation and toughness of the carbide-free bainite steel processed by the common isothermal quenching at 240 ℃.
TABLE 1 comparison of mechanical properties of bainite steels in conventional austempering and stacking fault energy control processes
Example 2:
a medium-low carbon carbide-free bainite steel comprises the following chemical components in percentage by weight: c: 0.32, Si: 1.65, Mn: 1.62, Cr: 1.23, Mo: 0.35, Al: 0.63, and the balance of Fe and a small amount of impurity elements. Tests show that the critical temperature of the composition steel for alternation of twinning and slip deformation is 400 ℃; the steel has 75% isothermal bainite phase transformation within 1h at 320 ℃. The specific process comprises the following steps: smelting the steel ingot with the components in an electric arc furnace, and then heating the steel ingot to 1200 ℃ for forging, wherein the finish forging temperature is not lower than 900 ℃. Austenitizing the steel at 920 ℃ for 30 minutes, controlling the temperature to be cooled to 530 ℃ for hot rolling for 30 percent, rapidly placing the steel in a salt bath furnace at 320 ℃ for isothermal 1 hour, performing 15 percent rolling deformation, and then air-cooling to room temperature.
The results of the drawing of the carbide-free bainitic steels treated by this process and the carbide-free bainitic steels austenitized at 920 ℃ for 30 minutes and then austempered at 350 ℃ are shown in table 2. The tensile strength, elongation and toughness of the carbide-free bainite steel processed by the process method are respectively improved by 45 percent, 12 percent and 45 percent compared with the tensile strength, elongation and toughness of the carbide-free bainite steel processed by the ordinary 350 ℃ isothermal quenching.
TABLE 2 comparison of mechanical properties of bainite steels in conventional austempering and stacking fault energy control processes
Example 3:
a medium-high carbon carbide-free bainite steel comprises the following chemical components in percentage by weight: c: 0.70, Si: 2.5, Mn: 0.62, Cr: 0.58 and the balance of Fe and a small amount of impurity elements. Tests show that the critical temperature of the composition steel for alternating twinning deformation and slip deformation is 250 ℃; the steel has isothermal bainite phase transformation of 65% in 3h at 200 ℃. The specific process comprises the following steps: smelting the steel ingot with the components in an electric arc furnace, and then heating the steel ingot to 1180 ℃ for forging, wherein the finish forging temperature is not lower than 900 ℃. Austenitizing the steel at 900 ℃ for 30 minutes, controlling the temperature to be cooled to 500 ℃ for hot rolling for 40 percent, rapidly placing the steel in a 200 ℃ salt bath furnace for isothermal 3 hours, then carrying out 8 percent rolling deformation, and then air cooling to room temperature.
The results of the drawing of the carbide-free bainitic steels treated by this process and the carbide-free bainitic steels austenitized at 920 ℃ for 30 minutes and then austempered at 250 ℃ for the usual time are shown in table 3. The tensile strength, elongation and toughness of the carbide-free bainite steel processed by the process method are respectively improved by 38 percent, 15 percent and 35 percent compared with the tensile strength, elongation and toughness of the carbide-free bainite steel processed by common isothermal quenching at 250 ℃.
TABLE 3 comparison of mechanical Properties of Bainite Steel in common isothermal quenching and adjustment and control of stacking fault energy
The above-mentioned embodiments are merely illustrative of the preferred embodiments of the present invention, and do not limit the scope of the present invention, and various modifications and improvements made to the technical solution of the present invention by those skilled in the art without departing from the spirit of the present invention shall fall within the protection scope defined by the claims of the present invention.
Claims (4)
1. A preparation method of ultrahigh-strength ductile bainite steel based on stacking fault energy regulation is characterized by comprising the following steps:
firstly, determining the fault energy of steel through testing or calculation, and determining a sliding deformation temperature interval and a twinning deformation temperature interval of the steel corresponding to the fault energy;
forging the steel, cooling to room temperature, heating to 900-1000 ℃, keeping the temperature for 20-60 min, carrying out austenitizing treatment, and then carrying out 20-40% deformation at 50-350 ℃ above the critical transformation temperature of the steel in which sliding deformation and twinning deformation are alternated;
and carrying out isothermal treatment in a bainite transformation temperature interval of the steel, so that after 50-80% of incomplete bainite transformation of the steel occurs, 5-20% of deformation is carried out in the twinning deformation temperature interval of the steel.
2. The method for preparing the ultra-high-strength ductile bainite steel based on the adjustment and control of the stacking fault energy according to claim 1, wherein the time for the isothermal treatment in the bainite transformation temperature interval of the steel is t, and the isothermal treatment is determined according to the time required for 50-80% incomplete bainite transformation of the steel at different temperatures in the bainite transformation temperature interval after testing the bainite transformation kinetics of the steel.
3. The preparation method of the ultra-high-strength ductile bainite steel based on the adjustment and control of stacking fault energy as claimed in claim 1, wherein the chemical composition range of main elements in the steel is as follows: 0.3-0.7 wt% of C and 1.5-2.5 wt% of Si, and the steel contains one or more of Mn, Cr, Ni, Mo and Al alloy elements.
4. The method for preparing the ultra-high-ductility bainite steel based on the stacking fault energy regulation and control as claimed in claim 1, wherein the ultra-high-ductility bainite steel contains 10-30% of residual austenite by volume.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114507803A (en) * | 2022-01-14 | 2022-05-17 | 西安建筑科技大学 | Quenching distribution steel with gradient distribution of stacking fault energy, preparation method and application |
| CN115725900A (en) * | 2022-11-14 | 2023-03-03 | 武汉科技大学 | High-strength and high-plasticity bainite steel and production method thereof |
| CN115874116A (en) * | 2022-12-27 | 2023-03-31 | 北京理工大学 | Silicon-aluminum-free superfine bainitic steel and preparation method thereof |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101235464A (en) * | 2007-11-29 | 2008-08-06 | 北京科技大学 | Copper and nickel alloying twin crystal inducing plasticity steel material and preparation technique |
| CN101927432A (en) * | 2009-06-25 | 2010-12-29 | 宝山钢铁股份有限公司 | Manufacturing method of high-manganese strip steel with high strength and plasticity |
| CN102321852A (en) * | 2011-09-01 | 2012-01-18 | 燕山大学 | Nanostructure carbide-free bainite medium-carbon alloy steel and preparation method |
| US20150110667A1 (en) * | 2013-10-21 | 2015-04-23 | Industry-Academic Cooperation Foundation, Yonsei University | High-strength and high-ductility steel sheet and method of manufacturing the same |
| CN106148660A (en) * | 2016-07-05 | 2016-11-23 | 中国科学院合肥物质科学研究院 | A kind of preparation method of deformed grains/partial, re-crystallization tissue twinning-induced plasticity steel |
| CN108118255A (en) * | 2018-01-08 | 2018-06-05 | 河北工业大学 | A kind of low temperature resistant steel of high manganese TWIP and its manufacturing method with high impact toughness |
| CN111546069A (en) * | 2020-05-11 | 2020-08-18 | 江苏联峰实业有限公司 | Residual stress eliminating method for hot-rolled high-strength steel |
-
2020
- 2020-09-28 CN CN202011042716.XA patent/CN112280941B/en active Active
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101235464A (en) * | 2007-11-29 | 2008-08-06 | 北京科技大学 | Copper and nickel alloying twin crystal inducing plasticity steel material and preparation technique |
| CN101927432A (en) * | 2009-06-25 | 2010-12-29 | 宝山钢铁股份有限公司 | Manufacturing method of high-manganese strip steel with high strength and plasticity |
| CN102321852A (en) * | 2011-09-01 | 2012-01-18 | 燕山大学 | Nanostructure carbide-free bainite medium-carbon alloy steel and preparation method |
| US20150110667A1 (en) * | 2013-10-21 | 2015-04-23 | Industry-Academic Cooperation Foundation, Yonsei University | High-strength and high-ductility steel sheet and method of manufacturing the same |
| CN106148660A (en) * | 2016-07-05 | 2016-11-23 | 中国科学院合肥物质科学研究院 | A kind of preparation method of deformed grains/partial, re-crystallization tissue twinning-induced plasticity steel |
| CN108118255A (en) * | 2018-01-08 | 2018-06-05 | 河北工业大学 | A kind of low temperature resistant steel of high manganese TWIP and its manufacturing method with high impact toughness |
| CN111546069A (en) * | 2020-05-11 | 2020-08-18 | 江苏联峰实业有限公司 | Residual stress eliminating method for hot-rolled high-strength steel |
Non-Patent Citations (1)
| Title |
|---|
| 李冬冬等: "Mn含量对Fe-Mn-C孪生诱发塑性钢拉伸变形行为的影响", 《金属学报》 * |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114507803A (en) * | 2022-01-14 | 2022-05-17 | 西安建筑科技大学 | Quenching distribution steel with gradient distribution of stacking fault energy, preparation method and application |
| CN114507803B (en) * | 2022-01-14 | 2022-09-20 | 西安建筑科技大学 | Quenching distribution steel with gradient distribution of fault energy, preparation method and application |
| CN115725900A (en) * | 2022-11-14 | 2023-03-03 | 武汉科技大学 | High-strength and high-plasticity bainite steel and production method thereof |
| CN115725900B (en) * | 2022-11-14 | 2023-10-24 | 武汉科技大学 | High-strength high-plasticity bainitic steel and production method thereof |
| CN115874116A (en) * | 2022-12-27 | 2023-03-31 | 北京理工大学 | Silicon-aluminum-free superfine bainitic steel and preparation method thereof |
| CN115874116B (en) * | 2022-12-27 | 2024-01-16 | 北京理工大学 | Silicon-aluminum-free superfine bainitic steel and preparation method thereof |
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