CN106011422A - High-strength steel with bimodal scale ferrite structure and low cost preparation method thereof - Google Patents
High-strength steel with bimodal scale ferrite structure and low cost preparation method thereof Download PDFInfo
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- CN106011422A CN106011422A CN201610628277.8A CN201610628277A CN106011422A CN 106011422 A CN106011422 A CN 106011422A CN 201610628277 A CN201610628277 A CN 201610628277A CN 106011422 A CN106011422 A CN 106011422A
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The invention discloses a high-strength steel with bimodal scale ferrite structure and a low cost preparation method thereof. Ordinary low carbon steel is adopted as a raw material plate, cold deformation and two-phase region quenching are carried out to obtain a bimodal scale structure with fine quasipolygonal ferrite grains distributed around coarse polygonal ferrite grains, the fine quasipolygonal ferrite grains plays a role of strengthening phase, and the coarse polygonal ferrite grains guarantee the steel plasticity. The high-strength steel prepared by the preparation method provided by the invention has excellent comprehensive mechanical properties, yield strength of greater than or equal to 650MPa, tensile strength of greater than or equal to 800MPa, uniform elongation of greater than or equal to 10.0%, a work hardening index of greater than or equal to 0.20, and a yield ratio of less than 0.90. At the same time, the process is simple and the production cost is low.
Description
Technical field
This patent disclosure relates generally to a kind of high-strength steel and preparation method thereof, particularly relate to one and there is bimodal yardstick ferrum
The high-strength steel of ferritic crystal grain distribution and low cost preparation method thereof.
Background technology
Advanced steel product be mainly characterized by Ultra-fine Grained, high-cleanness, high and high uniformity, its core theory and
Technology is to realize Ultra-fine Grained or the super fine organization of steel.At present, by controlled rolling and controlled cooling technique
Application, has been able to use Q235 ordinary low-carbon steel to produce the high-strength steel with super fine organization, its surrender
Intensity can realize doubling.But there are some researches show, ultra-fine grain or tissue also result in the processing hardening energy of steel
Power and uniform elongation reduce, and crack sensitivity increases, and limits the extension of its range of application.
Research for Cu alloy shows, by introducing size phase in the thin brilliant matrix of face-centered cubic alloy
To bigger crystal grain, it is thus achieved that bimodal grain size distribution, tiny crystal grain ensures that material has high intensity,
Bigger crystal grain then ensures that it is moulding, such that it is able to obtain more preferable intensity and plastic equilibrium.For iron and steel material
For material, realized the optimization of performance by the bimodal size distribution of single-phase crystal grain, be also beneficial to improve it resistance to
Corrosivity.
At present, by cold rolling or warm-rolling and the use of repeatedly heat treatment, it is possible to obtain bimodal size Ultra-fine Grained ferrum
The tissue of ferritic+diffusion carbide or " nano-carbide of bimodal ferrite crystal grain+uneven distribution " micro-
Fine grained texture, but its plasticity is the most poor, and uniform elongation is less than 6%, and process route is longer, produces
Process control difficulty is relatively big, limits further popularization and application.
Summary of the invention
It is an object of the invention to provide and a kind of there is high intensity, high-ductility, high work hardening index and low bend
By force than the 700MPa level high-strength steel of bimodal crystal particle scale distribution；On the technical problem to be solved in the present invention is
State the low cost preparation method of the high-strength steel with the distribution of bimodal crystal particle scale.
For solving above-mentioned technical problem, the technical solution used in the present invention is: cold rolling and biphase by plate
District's heat treatment, controls recrystallization process and the phase transition process of cold deformation crystal grain, it is thus achieved that the ferrite of different scale
Crystal grain.
The raw materials used plate of preparation method of the present invention is common low carbon steel plate；The matter of the chemical composition of described raw material plate
Amount percentage composition be: C 0.10%～0.20%, Si 0.10%～0.20%, Mn 0.60%～0.70%,
P≤0.015%, S≤0.01%, surplus is Fe and inevitable impurity, and organizational composition is ferrite and a small amount of
Pearlite.
Preparation method of the present invention includes that plate is cold rolling and a heat treatment step: described cold-rolling process: total deformation
Amount is not less than 50%；Described heat treatment uses tow-phase region heat treatment: holding temperature is positioned at two-phase section lower limit, right
Being 720-760 DEG C in ordinary low-carbon steel, temperature retention time is 5-60min, water-cooled.
The high-strength steel utilizing the preparation method of the present invention to prepare has the grain size distribution of bimodal yardstick, distribution
Peak value is respectively in 2-6 μm and 10-15 μm.Organizational structure be thick polygonal ferrite crystal grain and tiny standard many
Limit shape ferrite crystal grain is chimeric to coexist, and small grains is uniformly distributed in around coarse grain, and less crystal grain is (little
In 10 μm) area ratio shared in visual field is 45%-70%.
The high-strength steel utilizing the preparation method of the present invention to prepare has excellent comprehensive mechanical property, yield strength
>=650MPa, tensile strength >=800MPa, uniform elongation >=10.0%, work hardening index >=0.20, Qu Qiang
Ratio is less than 0.90.
Inventor it has further been found that when cold deformation cumulative deformation controls at 50-60%, heat treatment temperature
Taking 730-750 DEG C, temperature retention time is 10-30min, and the steel plate obtained after water-cooled has the most excellent comprehensive
Mechanical property, wherein average yield strength >=700MPa, tensile strength >=850MPa, also can guarantee that more simultaneously
High uniform elongation.This is likely due in above-mentioned technique interval tiny ferrum element in obtained structure of steel
Body crystal grain and thick ferrite crystal grain have reached optimum combination.
The present invention, only with a cold deformation and a Technology for Heating Processing, has just obtained having bimodal size distribution
The high-strength steel of single ferritic structure, raw materials used plate is with low cost, production technology is simple.
Accompanying drawing explanation
Fig. 1 be the present invention uses cold rolling rear two-phase section insulation 30min after quench the steel obtained tissue shine
Sheet.
Fig. 2 be the present invention uses cold rolling rear two-phase section insulation 30min after quench the crystal particle scale of the steel obtained
Distribution.
Fig. 3 be the present invention uses cold rolling rear 650 DEG C of insulation 30min after quench the tissue of the steel obtained.
Fig. 4 be the present invention uses cold rolling rear 800 DEG C of insulation 30min after quench the tissue of the steel obtained.
Fig. 5 be the present invention uses cold rolling rear 800 DEG C of insulation 30min after quench the crystal particle scale of the steel obtained
Distribution.
Fig. 6 be the present invention uses cold rolling rear 850 DEG C of insulation 5min after quench the tissue of the steel obtained.
Detailed description of the invention
Below by specific embodiment and combine accompanying drawing, to describe the present invention in detail, there is bimodal yardstick ferrite
The low cost preparation method of the high-strength steel of tissue.It should be appreciated by those skilled in the art that following embodiment is only
Exemplary illustration to the present invention, is not used for the present invention is carried out any restriction.
Embodiment 1
Raw material plate steel grade chemical composition is according to mass percentage: C 0.10%～0.20%, Si 0.10%～
0.20%, Mn 0.60%～0.70%, P≤0.015%, S≤0.01%, surplus is Fe and the most miscellaneous
Matter, sheet thickness 5.5mm, organizational composition is ferrite and a small amount of pearlite.
Cold-rolling mill is utilized to carry out cold roller and deformed, cumulative deformation 55%, then carry out a two-phase section quenching,
Specifically comprises the processes of: water-cooled at once after 750 DEG C of insulation 5min, i.e. can get the high strength steel plate of the present invention.
Fig. 1 is the macrograph of the high strength steel plate that the present embodiment obtains；As seen from Figure 1, this high strength steel plate
Be organized as thick polygonal ferrite crystal grain and tiny quasi-polygonal ferrite crystal grain the most embedding and, wherein
The area ratio shared in visual field less than the little crystal grain of 10 μm is about 68%.
Fig. 2 is the crystal particle scale distribution of the high strength steel plate that the present embodiment obtains, and double-scale crystal grain distribution peaks divides
Not in 3-6 μm and 10-13 μm.
Embodiment 2
The raw material plate used is with embodiment 1, the cumulative deformation 50% of cold-rolling process, and Technology for Heating Processing is:
At once water-cooled after 750 DEG C of insulation 15min.
The high strength steel plate obtained it be observed that and crystal particle scale analysis, and structure and crystal grain distribution are similar to Example 1,
Wherein shared in visual field less than the little crystal grain of 10 μm area ratio is about 59%.Double-scale crystal grain is distributed
Peak value is respectively in 3-5 μm and 11-15 μm.
Embodiment 3
The raw material plate used is with embodiment 1, the cumulative deformation 55% of cold-rolling process, and Technology for Heating Processing is:
At once water-cooled after 730 DEG C of insulation 30min.
The high strength steel plate obtained it be observed that and crystal particle scale analysis, and structure and crystal grain distribution are similar to Example 1,
Wherein shared in visual field less than the little crystal grain of 10 μm area ratio is about 45.5%.Double-scale crystal grain divides
Cloth peak value is respectively in 2-4 μm and 12-16 μm.
Embodiment 4
The raw material plate used is with embodiment 1, the cumulative deformation 60% of cold-rolling process, and Technology for Heating Processing is:
At once water-cooled after 740 DEG C of insulation 10min.
The high strength steel plate obtained it be observed that and crystal particle scale analysis, and structure and crystal grain distribution are similar to Example 1,
Wherein shared in visual field less than the little crystal grain of 10 μm area ratio is about 55.7%.Double-scale crystal grain divides
Cloth peak value is respectively in 3-5 μm and 12-15 μm.
Embodiment 5
The raw material plate used is with embodiment 1, the cumulative deformation 50% of cold-rolling process, and Technology for Heating Processing is:
At once water-cooled after 730 DEG C of insulation 20min.
The high strength steel plate obtained it be observed that and crystal particle scale analysis, and structure and crystal grain distribution are similar to Example 1,
Wherein shared in visual field less than the little crystal grain of 10 μm area ratio is about 47.2%.Double-scale crystal grain divides
Cloth peak value is respectively in 2-5 μm and 11-15 μm.
Embodiment 6
The raw material plate used is with embodiment 1, the cumulative deformation 55% of cold-rolling process, and Technology for Heating Processing is:
At once water-cooled after 750 DEG C of insulation 50min.
The high strength steel plate obtained it be observed that and crystal particle scale analysis, and structure and crystal grain distribution are similar to Example 1,
Wherein shared in visual field less than the little crystal grain of 10 μm area ratio is about 45%.Double-scale crystal grain is distributed
Peak value is respectively in 3-6 μm and 10-15 μm.
Embodiment 7
The raw material plate used is with embodiment 1, the cumulative deformation 55% of cold-rolling process, and Technology for Heating Processing is:
At once water-cooled after 760 DEG C of insulation 10min.
The high strength steel plate obtained it be observed that and crystal particle scale analysis, and structure and crystal grain distribution are similar to Example 1,
Wherein shared in visual field less than the little crystal grain of 10 μm area ratio is about 57.6%.Double-scale crystal grain divides
Cloth peak value is respectively in 3-6 μm and 11-15 μm.
Comparative example 1
The raw material plate used is with embodiment 1, the cumulative deformation 55% of cold-rolling process, and Technology for Heating Processing is:
At once water-cooled after 650 DEG C of insulation 15min.
Fig. 3 is the macrograph of the high strength steel plate that this comparative example obtains, and the steel plate obtained it be observed that and crystal grain chi
Degree analyze, organizational composition is the pearlite of uniform ferrite and nodularization, do not occur single ferrite and
The bimodal size distribution of its crystal grain.
Comparative example 2
The raw material plate used is with embodiment 1, the cumulative deformation 55% of cold-rolling process, and Technology for Heating Processing is:
At once water-cooled after 800 DEG C of insulation 30min.
Fig. 4 is the macrograph of the high strength steel plate that this comparative example obtains, Fig. 5 be the present embodiment obtain high-strength
The crystal particle scale distribution of steel plate, the steel plate obtained it be observed that and crystal particle scale analysis, and organizational composition is ferrite
And martensite, do not obtain single ferritic structure, the bimodal distribution of crystal particle scale does not occurs.
Comparative example 3
The raw material plate used is with embodiment 1, the cumulative deformation 55% of cold-rolling process, and Technology for Heating Processing is:
At once water-cooled after 850 DEG C of insulation 5min.
Fig. 6 is the macrograph of the high strength steel plate that this comparative example obtains, and the steel plate obtained it be observed that and crystal grain chi
Degree is analyzed, and organizational composition is martensite and minimal amount of ferrite, does not obtain single ferritic structure and crystalline substance
The bimodal size distribution of grain.
The steel plate sample that the various embodiments described above and comparative example obtain detects according to concerned countries standard, detection
The results are shown in Table 1.
Table 1: properties of sample
| Sample | Yield strength/MPa | Tensile strength/MPa | Uniform elongation/% | Work hardening index | Yield tensile ratio |
| Embodiment 1 | 793 | 964 | 11.32 | 0.23 | 0.82 |
| Embodiment 2 | 798 | 949 | 11.44 | 0.22 | 0.84 |
| Embodiment 3 | 714 | 868 | 12.53 | 0.22 | 0.82 |
| Embodiment 4 | 746 | 893 | 11.23 | 0.24 | 0.84 |
| Embodiment 5 | 711 | 873 | 12.15 | 0.22 | 0.81 |
| Embodiment 6 | 801 | 912 | 10.11 | 0.23 | 0.88 |
| Embodiment 7 | 785 | 937 | 10.42 | 0.23 | 0.84 |
| Comparative example 1 | 411 | 526 | 24.74 | 0.17 | 0.78 |
| Comparative example 2 | 639 | 735 | 10.02 | 0.21 | 0.87 |
| Comparative example 3 | 678 | 723 | 9.87 | 0.17 | 0.94 |
Claims (5)
1. there is a low cost preparation method for the high-strength steel of bimodal yardstick ferritic structure, with the lowest
Carbon steel is raw material plate, prepares described high-strength steel through cold deformation and a heat treatment step；Wherein
The chemical composition weight/mass percentage composition of raw material plate used is: C 0.10%～0.20%, Si 0.10%～
0.20%, Mn 0.60%～0.70%, P≤0.015%, S≤0.01%, surplus is Fe and the most miscellaneous
Matter, its organizational composition is ferrite+a small amount of pearlite；
Described cold deformation is cold roller and deformed, and total deformation is 50%-70%；
A described heat treatment is two-phase section Quenching Treatment, at the two-phase section lower limit temperature of ordinary low-carbon steel
Water-cooled after 720～760 DEG C of insulations 5～60min.
2. there is a high-strength steel for bimodal yardstick ferritic structure, by the low cost described in claim 1
Preparation method prepare, described high-strength steel be organized as thick polygonal ferrite crystal grain and tiny quasi-polygon ferrum
Ferritic crystal grain is chimeric to coexist, and small grains is uniformly distributed in around coarse grain, and crystallite dimension has bimodal chi
Degree distribution.
The high-strength steel with bimodal yardstick ferritic structure the most according to claim 2, described high-strength
Crystalline grain of steel distribution of sizes peak value is respectively in 2-6 μm and 10-15 μm.
The high-strength steel with bimodal yardstick ferritic structure the most according to claim 2, described high-strength
Area ratio shared in visual field less than the little crystal grain of 10 μm in steel is 45%-70%.
The high-strength steel with bimodal yardstick ferritic structure the most according to claim 2, described high-strength
The mechanical performance index of steel is: yield strength >=650MPa, tensile strength >=800MPa, uniform elongation
>=10%, work hardening index is more than 0.2, and yield tensile ratio is less than 0.9.
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110055379A (en) * | 2019-06-03 | 2019-07-26 | 郑州航空工业管理学院 | A kind of preparation method of micro- multi-layer sheet structure steel plate |
| CN110863084A (en) * | 2018-08-28 | 2020-03-06 | 南京理工大学 | Processing method for regulating ductility and toughness of dual-phase steel material through surface strong plastic deformation |
| CN114622074A (en) * | 2022-05-12 | 2022-06-14 | 中北大学 | Austenitic stainless steel, heat treatment process thereof and application of heat treatment process |
| US11549157B2 (en) | 2017-07-19 | 2023-01-10 | Shiv Nadar University | Method for modifying surface grain structure of the material and apparatus thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| US11549157B2 (en) | 2017-07-19 | 2023-01-10 | Shiv Nadar University | Method for modifying surface grain structure of the material and apparatus thereof |
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| CN114622074A (en) * | 2022-05-12 | 2022-06-14 | 中北大学 | Austenitic stainless steel, heat treatment process thereof and application of heat treatment process |
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| CN106011422B (en) | 2018-01-30 |
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Effective date of registration: 20200811 Address after: 225300 Sanshe Village, Zhangguo Town, Xinghua City, Taizhou City, Jiangsu Province Patentee after: XINGHUA YINLONG STAINLESS STEEL PRODUCTS Co.,Ltd. Address before: 063000 No. 38 Hua Yan Road, North Tangshan City Road, Hebei Patentee before: TANGSHAN College |
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