AU2021332868A9 - Gpa-grade bainite steel having ultra-high yield ratio and manufacturing method for gpa-grade bainite steel - Google Patents
Gpa-grade bainite steel having ultra-high yield ratio and manufacturing method for gpa-grade bainite steel Download PDFInfo
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- AU2021332868A9 AU2021332868A9 AU2021332868A AU2021332868A AU2021332868A9 AU 2021332868 A9 AU2021332868 A9 AU 2021332868A9 AU 2021332868 A AU2021332868 A AU 2021332868A AU 2021332868 A AU2021332868 A AU 2021332868A AU 2021332868 A9 AU2021332868 A9 AU 2021332868A9
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 211
- 239000010959 steel Substances 0.000 title claims abstract description 211
- 229910001563 bainite Inorganic materials 0.000 title claims abstract description 136
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 30
- 238000000034 method Methods 0.000 claims abstract description 39
- 230000008569 process Effects 0.000 claims abstract description 34
- 229910052729 chemical element Inorganic materials 0.000 claims abstract description 24
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 23
- 238000000137 annealing Methods 0.000 claims abstract description 22
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 18
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 18
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 16
- 238000001816 cooling Methods 0.000 claims description 100
- 238000010438 heat treatment Methods 0.000 claims description 25
- 238000002791 soaking Methods 0.000 claims description 20
- 238000005096 rolling process Methods 0.000 claims description 19
- 239000002244 precipitate Substances 0.000 claims description 17
- 238000010583 slow cooling Methods 0.000 claims description 13
- 239000012535 impurity Substances 0.000 claims description 9
- 238000005097 cold rolling Methods 0.000 claims description 8
- 229910052720 vanadium Inorganic materials 0.000 claims description 5
- 238000003723 Smelting Methods 0.000 claims description 4
- 238000005266 casting Methods 0.000 claims description 4
- 238000005098 hot rolling Methods 0.000 claims description 4
- 238000005554 pickling Methods 0.000 claims description 4
- 230000009467 reduction Effects 0.000 claims description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 3
- 229910052799 carbon Inorganic materials 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 2
- CJYDNDLQIIGSTH-UHFFFAOYSA-N 1-(3,5,7-trinitro-1,3,5,7-tetrazocan-1-yl)ethanone Chemical compound CC(=O)N1CN([N+]([O-])=O)CN([N+]([O-])=O)CN([N+]([O-])=O)C1 CJYDNDLQIIGSTH-UHFFFAOYSA-N 0.000 claims 1
- 230000000052 comparative effect Effects 0.000 description 37
- 238000005452 bending Methods 0.000 description 17
- 239000000203 mixture Substances 0.000 description 15
- 229910000734 martensite Inorganic materials 0.000 description 12
- 229910045601 alloy Inorganic materials 0.000 description 10
- 239000000956 alloy Substances 0.000 description 10
- 238000013461 design Methods 0.000 description 10
- 239000000243 solution Substances 0.000 description 9
- 230000009466 transformation Effects 0.000 description 9
- 239000011159 matrix material Substances 0.000 description 8
- 150000001247 metal acetylides Chemical class 0.000 description 8
- 238000012360 testing method Methods 0.000 description 8
- 229910000859 α-Fe Inorganic materials 0.000 description 8
- 239000000463 material Substances 0.000 description 7
- 238000001556 precipitation Methods 0.000 description 7
- 239000000126 substance Substances 0.000 description 7
- 230000001965 increasing effect Effects 0.000 description 6
- 230000015572 biosynthetic process Effects 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 229910001566 austenite Inorganic materials 0.000 description 4
- 230000000717 retained effect Effects 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- 229910000797 Ultra-high-strength steel Inorganic materials 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 3
- 239000010960 cold rolled steel Substances 0.000 description 3
- 230000001276 controlling effect Effects 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 3
- 238000011056 performance test Methods 0.000 description 3
- 230000002829 reductive effect Effects 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 229910000885 Dual-phase steel Inorganic materials 0.000 description 2
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N Iron oxide Chemical compound [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 description 2
- VCUFZILGIRCDQQ-KRWDZBQOSA-N N-[[(5S)-2-oxo-3-(2-oxo-3H-1,3-benzoxazol-6-yl)-1,3-oxazolidin-5-yl]methyl]-2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidine-5-carboxamide Chemical compound O=C1O[C@H](CN1C1=CC2=C(NC(O2)=O)C=C1)CNC(=O)C=1C=NC(=NC=1)NCC1=CC(=CC=C1)OC(F)(F)F VCUFZILGIRCDQQ-KRWDZBQOSA-N 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 238000006392 deoxygenation reaction Methods 0.000 description 2
- 230000002542 deteriorative effect Effects 0.000 description 2
- 229910001562 pearlite Inorganic materials 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 238000009628 steelmaking Methods 0.000 description 2
- 238000010998 test method Methods 0.000 description 2
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- 229910052684 Cerium Inorganic materials 0.000 description 1
- 241000282376 Panthera tigris Species 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 239000010962 carbon steel Substances 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 230000008094 contradictory effect Effects 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 230000003635 deoxygenating effect Effects 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 238000011534 incubation Methods 0.000 description 1
- 230000001939 inductive effect Effects 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000003672 processing method Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 238000000638 solvent extraction Methods 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 239000002699 waste material Substances 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- 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
- B21C47/02—Winding-up or coiling
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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
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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
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- C21D1/26—Methods of annealing
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- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/84—Controlled slow cooling
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- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
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- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- C21D6/008—Heat treatment of ferrous alloys containing Si
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- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- 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
- C21D8/0273—Final recrystallisation annealing
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
- C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
- C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
- C23G1/08—Iron or steel
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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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
- C21D2211/00—Microstructure comprising significant phases
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Abstract
GPa-grade bainite steel having an ultra-high yield ratio, containing, in addition to Fe, the following chemical elements in mass percentages: 0.12-0.24% of C; 0.2-0.5% of Si; 1.3-2.0% of Mn; 0.001-0.004% of B; 0.01-0.05% of Al; and at least one of Cr, Nb, Ti, and Mo, wherein Cr≤0.4%, Nb≤0.06%, Ti≤0.1%, and Mo≤0.4%. Also disclosed are a manufacturing method and annealing process for the steel.
Description
Technical Field The present disclosure relates to a steel and a method for manufacturing the same, in particular to a GPa-grade bainite steel and a method for manufacturing the same.
Background Art Under the new-era concept of "green-safety", GPa-grade high-strength steel has become one of the automotive structural materials that attracts the most interest of the major automobile manufacturers as higher and higher strength is required for structural parts and safety parts of automobiles. In recent years, more and more automotive structural parts (e.g. components of the cockpit and chassis system) are required to ensure "zero deformation" during service to guarantee proper use of the automobile and safety of the driver and passengers. This imposes very high requirements on the material. Particularly, it is required to have yield strength or yield ratio as high as possible. At present, high-yield-strength or high-yield-ratio materials have attracted more and more attention from automobile manufacturers. The market demand for high-yield-strength or high-yield-ratio GPa grade steel has also increased day by day. The yield ratio of the GPa-grade high-strength steel mentioned in the existing patents for invention is generally not high. The yield ratio of the dual-phase steel accounting for 90% of the market share of the GPa-grade automotive high-strength steel is only 0.6-0.75. For the rest products accounting for a small proportion, such as martensite steel, quenching-partitioning steel (Q&P steel), and complex phase steel, although the yield ratio has been increased slightly, it is only about 0.75 0.85. For example, the Chinese patent document CN103361577A (published on October 23, 2013 and titled "HIGH-YIELD-RATIO AND HIGH-STRENGTH STEEL SHEET HAVING EXCELLENT PROCESSABILITY") discloses a high-yield-ratio and high-strength steel sheet having a microstructure dominated by ferrite, martensite, tempered martensite and bainite. Its tensile strength can reach 980 MPa or higher, but its yield ratio is only >0.68, which still fails to meet the latest requirement of the automotive parts market for high-yield-ratio GPa-grade steel sheets. For another example, the Chinese patent document CN106170574A (published on November , 2016 and titled "HIGH-YIELD-RATIO AND HIGH-STRENGTH COLD-ROLLED STEEL SHEET AND MANUFACTURING METHOD THEREFOR") discloses a high-yield-ratio and high-strength cold-rolled steel sheet and a manufacturing method therefor. The structure of the steel sheet mainly contains ferrite, retained austenite, martensite and trace amounts of bainite and tempered ferrite. Its tensile strength can reach 980 MPa or higher, but its yield ratio is only > 0.75, no more than 0.8 at most. The market demand for GPa-grade high-strength steel having a yield ratio > 0.9 still cannot be satisfied. On the other hand, although some patent documents disclose high-yield-ratio steel sheets having a yield ratio > 0.9 and manufacturing methods therefor, the tensile strength of the steel sheets disclosed by these patent documents cannot reach the level of 980 MPa. For example, the Chinese patent document CN102719736A (published on October 10, 2012 and titled ULTRAFINEE GRAIN SLIDEWAY STEEL HAVING YIELD RATIO > 0.9 AND PRODUCTION METHOD THEREFOR") discloses a steel sheet having a yield ratio > 0.9 obtained by forming an ultrafine grain structure, but its tensile strength is only at the level of 700 MPa. As it can be seen, for a steel sheet at the present stage, the tensile strength reaching the GPa grade and the yield ratio > 0.9 are two contradictory technical indicators. The technical problem behind this contradiction is that it is technically very difficult to achieve an ultra-high yield ratio of >0.9 by regulating the structure. First of all, to achieve a high yield ratio, the structure of the matrix in the steel sheet needs to be relatively uniform. For example, the matrix consists of pure bainite or pure martensite. If the steel sheet has a multi-phase or complex-phase matrix structure, such as a matrix structure containing ferrite, retained austenite, tempered martensite and martensite at the same time, it is not easy to obtain a high yield ratio. However, if it's desired that the strength of the steel sheet reaches the GPa level, the mutual cooperation of multiple phases in the structure is often required, such as in the typical ferrite/martensite dual-phase steel and the advanced high-strength steel that contains retained austenite and incorporates the TRIP effect. This is the first aspect of the technical contradiction. However, even with a pure bainite or martensite structure, due to dislocation slip and work hardening caused by processing strain, it's difficult for the yield ratio of the steel sheet to reach > 0.9. Generally speaking, the yield ratio of a steel sheet having a pure martensite or bainite matrix is about 0.8-0.9. Therefore, in order to further obtain a steel sheet having an ultra-high yield ratio, it is necessary to further design a complex composition and a complex process to prevent dislocation slip and increase the yield strength of the material. For example, the Chinese patent document CN101910436A (published on December 8,2010 and titled "HIGH-STRENGTH COLD-ROLLED STEEL SHEET HAVING EXCELLENT WEATHER RESISTANCE AND PREPARATION METHOD THEREFOR") discloses a method for increasing the yield strength of a material by introducing a large amount of expensive solid solution alloy elements Cr, Zr, Co, W, etc. However, considering that the process for preparing the existing GPa-grade ultra-high-strength steel is complicated and the amount of alloy elements added to it is already very high, it is still considerably doubtful whether the above complicated process technology or the addition of expensive alloy elements for further increasing the yield ratio is suitable for combining with the existing GPa-grade ultra-high-strength steel whose structure is already extremely complex. This is the second aspect of the technical contradiction. Therefore, a series of technical difficulties such as the first and second technical contradictions mentioned above have to be overcome in order to obtain GPa-grade ultra-high-strength steel having a yield ratio of > 0.9. This cannot be realized by the existing patent technology. As such, in order to solve the above problem, it is desirable to obtain a GPa-grade bainite steel having an ultra-high yield ratio. This GPa-grade bainite steel has an ultra-high yield ratio, an ultra high strength, and excellent hole-expanding and bending performances at the same time. It can be used to prepare automotive structural parts, and realize the new design concept of "green-safety" for automobiles.
Summary One object of the present disclosure is to provide a GPa-grade bainite steel having an ultra high yield ratio. According to the present disclosure, a GPa-grade bainite steel having an ultra-high yield ratio can be obtained by an appropriate design of the chemical composition. The GPa-grade bainite steel has a tensile strength of > 980 MPa, a yield strength of > 900MPa, a yield ratio of > 0.9, and a hole expansion rate of > 55%. It has an ultra-high yield ratio, an ultra-high strength, and excellent hole-expanding and bending performances at the same time. It can be used to prepare automotive structural parts, and has good popularization prospect and application value. In order to achieve the above object, the present disclosure proposes a GPa-grade bainite steel having an ultra-high yield ratio, comprising the following chemical elements in mass percentages in addition to Fe and unavoidable impurities: C: 0.12-0.24%; Si: 0.2-0.5%; Mn: 1.3-2.0%; B: 0.001-0.004%; Al: 0.01-0.05%; at least one of Cr, Nb, Ti and Mo, wherein Cr<0.4%, Nb0.06%, Ti<01%, Mo<0.4%. Further, in the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure, the mass percentages of the chemical element are: C: 0.12-0.24%;
Si: 0.2-0.5%; Mn: 1.3-2.0%; B: 0.001-0.004%; Al: 0.01-0.05%; at least one of Cr, Nb, Ti and Mo, wherein Cr<0.4%, Nb<0.06%, Ti<01%, Mo<0.4%; a balance of Fe and other unavoidable impurities. The principles for designing the various chemical elements in the technical solution of the present disclosure will be described in detail as follows: C: In the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure, element C is one of the key elements that control the phase transformation of the structure in the carbon steel. Meanwhile, element C has a great influence on the strength of the steel sheet. Element C can form alloy carbides with other alloy elements, thereby increasing the strength of the steel sheet. If the content of element C in the steel is lower than 0.12%, the strength of the steel will not meet the target requirement; and if the content of element C in the steel is higher than 0.24%, it is easy to form martensite structure and coarse cementite which will deteriorate the performances of the steel sheet. As such, in the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure, the mass percentage of C is controlled at 0. 12 - 0 .2 4 %. Of course, in some preferred embodiments, in order to obtain better implementation effects, the mass percentage of element C may be controlled at 0.15-0.20%. Si: In the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure, element Si is an essential element for deoxygenation in steelmaking. It has a certain solid solution strengthening effect, and at the same time, it also has a certain influence on the formation of bainite (the more element B in the steel, the easier it is to form carbon-free bainite). It should be noted that when the content of element Si in the steel is lower than 0.2%, it is difficult to achieve sufficient deoxygenation effect; and when the content of element Si in the steel is higher than 0.5%, it is easy to form iron oxide scale or tiger stripe color difference, which is not conducive to the surface quality of steel sheets for automobiles. As such, in the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure, the mass percentage of Si is controlled at 0.2-0.5%. Mn: In the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure, element Mn is the main additive element, and it is one of the key elements that control the phase transformation of the structure in the steel. It should be noted that element Mn is low in cost. It is not only an element for effectively improving the strength of the steel, but also an important element for solid solution strengthening. However, it should be noticed that the content of element Mn in the steel should not be too high. When the content of element Mn in the steel is too high, it will deteriorate the corrosion resistance and welding performance, aggravate the tendency of grain coarsening, and reduce the plasticity and toughness of the steel. As such, in the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure, the mass percentage of Mn is controlled at 1.3-2.0%. Of course, in some preferred embodiments, in order to obtain better implementation effects, the mass percentage of element Mn may be controlled at 1.6-2. 0 %. B: In the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure, element B is not only beneficial to the formation of bainite in the steel, but also has a significant influence on the strength and hardness of the steel sheet. It should be noted that if the content of element B in the steel is lower than 0.001%, the strength of the steel will not meet the target requirement; and if the content of element B in the steel is higher than 0.004%, it is easy to form brittle borides which will affect the hole-expanding and bending performances of the steel sheet. As such, in the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure, the mass percentage of B is controlled at 0.001-0.004%. Al: In the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure, element Al is only added to the steel as a deoxygenating element. It can remove element o from the steel to ensure the performances and quality of the steel. As such, in the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure, the mass percentage of Al is controlled at 0.01-0.05%. In some existing technologies, element Al is added to steel in a large amount (>0.1%) as an element for forming ferrite and inhibiting carbide precipitation in an attempt to effectuate solid solution strengthening, or to change the phase transformation temperature, bainite formation kinetics and carbide precipitation kinetics by adding Al, so as to change the phase transformation of the steel to form retained austenite or carbon-free bainite, thereby improving the strength of the steel ultimately. However, the composition control and process adjustment proposed according to the present disclosure can already provide a GPa-grade bainite steel having an ultra high yield ratio, so there is no need to add a large amount of element Al, thereby avoiding cost increase and greatly increased difficulty in steelmaking and manufacturing. Ti, Cr, Nb and Mo: In the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure, Ti, Cr, Nb and Mo are optional alloy elements that can be added to the steel to form a second phase of dispersed fine carbide which precipitates to further improve the strength and yield ratio of the steel sheet. In addition, it should be noted that elements Cr and Mo can prolong the incubation period of pearlite and ferrite in the CCT curve, inhibit the formation of pearlite and ferrite, and make it easier to obtain the bainite structure during cooling, which is beneficial to improve the hole expansion rate of the steel. As it can be seen, the above four alloy elements have an influence on both the regulation of the structure of the steel sheet and the corresponding annealing process. The factors that influence the formation of carbides have a direct influence on the proportion and morphology of the carbides that are formed. As such, in the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure, the mass percentage of Cr, Nb, Ti and Mo are respectively controlled as follows: Cr0.4%, Nb<O.06%, Ti<0.%, Mo<0.4%. On the other hand, the addition of the above alloy elements will increase the material cost. To balance the performances and the cost control, in the technical solution according to the present disclosure, it is preferable to add at least one of Cr, Nb, Ti and Mo to the steel. In some preferred embodiments, the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure comprises at least 0.1-0.4% Cr. In some preferred embodiments, the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure comprises at least 0.1-0.4% Mo. In some preferred embodiments, the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure comprises at least one or both of Cr and Mo. In some preferred embodiments, the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure comprises at least 0.1-0.4% Cr and 0.1-0.4% Mo. Further, in the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure, the mass percentages of the chemical elements satisfy at least one of the following: C: 0.15-0.20%, Mn: 1.6-2.0%. Further, in the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure, among the other unavoidable impurities: P < 0.015%; and/or S < 0.004%. In the above technical solution, both P and S are impurity elements in the steel. If the technical conditions permit, in order to obtain a quenched and tempered steel having better performances and better quality, the amount of impurity elements in the steel should be minimized. Further, the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure further comprises at least one of the following chemical elements: 0<Cus0.2%, 0 O<Ni<0.2%, 0<V<0.2%, 0<Ce<0.2%. In the technical solution according to the present disclosure, each of the above Cu, Ni, V and Ce elements can further improve the performances of the GPa-grade bainite steel having an ultra high yield ratio according to the present disclosure. Further, the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure satisfies 0.18<M<0.27, wherein M=Cr/2.5+Ti+V/5+Nb/1.7+Mo/1.7, wherein Cr, V, Nb, Ti and Mo each represent the value in front of the percent sign in the mass percentage of each chemical element. In the above technical solution, it should be noted that in the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure, while the mass percentages of the chemical elements are controlled respectively, in order to impart better performances and quality to the GPa grade bainite steel, it's preferred to further control M to be 0.18<M<0.27, wherein M=Cr/2.5+Ti+V/5+Nb/1.7+Mo/1.7, wherein Cr, V, Nb, Ti and Mo each represent the value in front of the percent sign in the mass percentage of each chemical element. It should be noted that in the present disclosure, if M is too high, it will be easy to form coarse carbides which will deteriorate the hole expansion rate and bending performance of the steel; and if M is too low, the carbide precipitate phase cannot be formed sufficiently, so that the strength and yield ratio of the steel will be insufficient. Therefore, in the present disclosure, M may be controlled to be 0.18<M<0.27, so as to ensure dispersive precipitation of nano-, submicron- or micron-scale granular carbides in the steel, and ensure a maximum diameter of the granular carbide precipitate. Further, the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure satisfies 0.20<Cb<0.27, wherein the equivalent bainite carbon content C=C-(Mo+Nb)/8 (Ti+V)/4-Cr/12+Ni/10+Mn/20+Bx10, wherein each element in the formula represents the value in front of the percent sign in the mass percentage of the element. In the above technical solution, in the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure, since the alloy elements and the M value have an influence on the precipitation of carbides, they will indirectly influence the equivalent bainite carbon content Cb in the steel. It should be noted that in the present disclosure, if Cb is too low, a single bainite matrix structure cannot be formed in a sufficient amount; and if Cb is too high, the hardness of bainite will be too large, thereby deteriorating the bending and hole-expanding performances of the steel. Therefore, in the present disclosure, while the mass percentages of the chemical elements are controlled respectively, it's preferred to further control C to be 0.20Cb<-0.27, so as to effectively ensure that the phase proportion of acicular lower bainite in the steel is >90%. Furthermore, in the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure, its microstructure is mainly acicular lower bainite, and the phase proportion of the acicular lower bainite is > 90%. Further, in the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure, its microstructure further comprises a nano-, submicron- or micron-scale granular carbide precipitate phase that is precipitated dispersively, and a total phase proportion of the granular carbide precipitate phase + acicular lower bainite is >99%. Furthermore, in the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure, the granular carbide precipitate has a maximum diameter of <2 m. Further, the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure has a tensile strength of >980 MPa, preferably >1000 MPa, a yield strength of >900 MPa, preferably >950 MPa, a yield ratio of >0.9, preferably > 0.95, and a hole expansion rate of > 55%, preferably > 60%. In a preferred embodiment, the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure has a tensile strength of > 1000 MPa, a yield strength of > 910 MPa, a yield ratio of > 0.9, and a hole expansion rate of >55%. Further, the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure has a yield strength of >950 MPa, a yield ratio of > 0.95, and further preferably a tensile strength of >1000 MPa, and a hole expansion rate of > 60%. Further, the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure has an elongation of >9.0%. Correspondingly, another object of the present disclosure is to provide an annealing process for the above GPa-grade bainite steel having an ultra-high yield ratio. This annealing process plays a key role for the performances of the steel. By designing the process appropriately and controlling relevant process parameters, the GPa-grade bainite steel having an ultra-high yield ratio can be obtained. In order to achieve the above object, the present disclosure proposes an annealing process for the above GPa-grade bainite steel having an ultra-high yield ratio, comprising steps of: (a) Heating to a soaking temperature Ts at a heating rate of 50°C /s at a heating stage, wherein Ts is 840-900 °C; (b) Holding the temperature Ts for 5 minutes or less at a soaking stage; (c) Cooling to (Ts-80) to (Ts-140) °C at a first cooling rate of <15°C /s at a slow cooling stage; (d) Cooling to (Ts-490) to (Ts-440) °C at a second cooling rate of >(130-Q)°C/s at a fast cooling stage, wherein Q=Cx180+Six10+Mnx3O+Nix5O+Crx15+Mox15+Bx2000, wherein each element in the formula represents the value in front of the percent sign in the mass percentage of the element; (e) Cooling at a third cooling rate for 10-40 s at a controlled cooling stage for self-temperature rise, wherein [(Q-80)/12]<third cooling rate<[(Q-80)/8]; (f) Finally, cooling the strip steel in air to room temperature at an air cooling stage. In the technical solution according to the present disclosure, it should be noted that the above annealing process comprises a heating stage, a soaking stage, a slow cooling stage, a fast cooling stage, a controlled cooling stage for self-temperature rise, and an air cooling stage. It plays a key role for the performances of the GPa-grade bainite steel according to the present disclosure. In step (a), at the heating stage, it is necessary to ensure heating at a heating rate of 50°C/s to a soaking temperature Ts: 840-900 °C, preferably heating to a soaking temperature of 840-870 °C. The heating rate at the heating stage should not be too high; otherwise, the uniformity of the structure of the strip steel will be reduced. In addition, it should be noted that if the soaking temperature Ts is lower than the soaking temperature range designed above, the strip steel cannot acquire >90% acicular lower bainite structure; and if the soaking temperature Ts is higher than the soaking temperature range designed above, the grains in the strip steel will be coarse, which will deteriorate the formability of the steel. In some embodiments, the heating rate in step (a) is 5-45 °C/s. In step (b), the soaking time is preferably not less than 1 minute. For example, the soaking time is 1 minute to 4.5 minutes. In step (c), it's necessary to cool the strip steel to (Ts-80) to (Ts-140) °C at a first cooling rate of <15°C/s at the slow cooling stage. The first cooling rate at the slow cooling stage should not be too high; otherwise, not only energy waste, but also nonuniform structure of the strip steel will be resulted. In addition, it should be noted that if the slow cooling temperature is lower than the slow cooling temperature range designed above, the strip steel cannot acquire >90% bainite structure; and if the slow cooling temperature is higher than the slow cooling temperature range designed above, a higher cooling capacity and a higher temperature precision control capability will be required at the subsequent fast cooling stage, because the structure uniformity of the strip steel will be deteriorated, and in turn, the performances of the product will be deteriorated if the cooling capacity or temperature precision control capability is insufficient. Preferably, the first cooling rate in step (c) is 5-15 °C/s, preferably 5-12 °C/s. In step (d), at the fast cooling stage, it's necessary to cool the strip steel to (Ts-490) to (Ts-440) C at a second cooling rate of >(130-Q) °C/s; wherein Q=Cx180 +Six10+Mnx30+Nix5+Crx15+Mox15+Bx2000. If the second cooling rate at the fast cooling stage is insufficient, or the cooling temperature is higher than (Ts-440) °C, bainite transformation will occur prematurely, and a high-temperature bainite structure (such as upper bainite or equiaxed bainite) will be formed. As a result, not only a phase proportion of >90% of acicular lower bainite in the steel cannot be guaranteed, but the latent heat of phase transformation will also be reduced greatly, so that subsequent controlled cooling for self-temperature rise cannot be implemented. Thus, the material structure will be abnormal, and the steel sheet and steel strip cannot acquire an ultra high yield ratio. Nevertheless, if the cooling temperature at the fast cooling stage is lower than (Ts 490) °C, a martensite structure will be formed, and thus the hole expansion rate and bending performance of the steel will be reduced. In step (e), at the controlled cooling stage for self-temperature rise, if the strip steel can be treated according to the designed parameters at the fast cooling stage, the self-temperature rise phenomenon will occur to the strip steel due to the release of a large quantity of the latent heat of phase transformation. The self-temperature rise can increase the temperature of the strip steel by 50 120 0C rapidly, uniformly and efficiently, thereby promoting uniform and dispersive precipitation of carbides. In order to ensure full carbide precipitation and small precipitate size, it is necessary to control the temperature of the strip steel and cool it at a third cooling rate for 10-40s, wherein [(Q )/12]<third cooling rate<[(Q-80)/8].
It should be noted that if the third cooling rate is too low or the cooling time is too long at the controlled cooling stage for self-temperature rise, failing to meet the above design requirements according to the present disclosure, carbide precipitate tends to be coarsened, thereby deteriorating the hole expansion rate and bending performance; and if the third cooling rate is too high or the cooling time is too short, it's likely that carbides cannot precipitate fully, so that the steel cannot acquire an ultra-high yield ratio, i.e. a yield ratio of > 0.9. In addition, still another object of the present disclosure is to provide a manufacturing method for the above GPa-grade bainite steel having an ultra-high yield ratio. With the use of this manufacturing method, the GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure can be made effectively. In order to achieve the above object, the present disclosure proposes a manufacturing method for the above GPa-grade bainite steel having an ultra-high yield ratio, comprising steps of: (1) Smelting and casting; (2) Hot rolling; (3) Post-rolling cooling and coiling; (4) Pickling and cold rolling; (5) The above annealing process. In the technical solution according to the present disclosure, in the above manufacturing method, the main purpose of steps (1)-(4) before the annealing process is to obtain a steel sheet or steel strip having a uniform composition and a uniform initial structure, so as to ensure that the uniformity and stability of the structure and performances can be satisfied in the subsequent annealing process. The annealing process in step (5) plays a key role for the performances of the steel sheet. Further, in the manufacturing method according to the present disclosure, in step (2), a heating temperature is controlled at 1150-1260 °C; an initial rolling temperature of finishing rolling is controlled at 1100-1220 °C; and a final rolling temperature of finishing rolling is controlled at 900 950 °C. Further, in the manufacturing method according to the present disclosure, in step (3), a cooling rate is controlled at 30-150 °C/s, and a coiling temperature is controlled at 450-580 °C. Further, in the manufacturing method according to the present disclosure, in step (4), a cold rolling reduction rate is controlled at > 50%. Further, in the manufacturing method according to the present disclosure, the GPa-grade bainite steel having an ultra-high yield ratio is the GPa-grade bainite steel having an ultra-high yield ratio described in any embodiment herein. Compared with the prior art, the GPa-grade bainite steel having an ultra-high yield ratio and the method of manufacturing the same according to the present disclosure have the following advantages and beneficial effects: On the premise of ensuring that the composition of chemical elements and the process are relatively simple and controllable, the present disclosure optimizes the combination of alloy elements, and adjusts the annealing process in an innovative way. On the basis of ensuring that the matrix structure of the steel sheet is a simple and single bainite structure, the release of the latent heat of phase transformation is introduced to realize self-temperature rise of the steel strip. This not only reduces energy consumption, but also realizes fast, uniform and efficient control of the temperature rise of the steel strip, thereby inducing dispersive precipitation of the fine second phase. Thus, a GPa-grade bainite steel having an ultra-high yield ratio and good formability is obtained. By designing the chemical composition appropriately according to the present disclosure, a GPa-grade bainite steel having an ultra-high yield ratio that has a tensile strength of > 980 MPa, a yield strength of > 900 MPa, a yield ratio of > 0.9, and a hole expansion rate of > 55% can be obtained. The GPa-grade bainite steel has an ultra-high yield ratio, an ultra-high strength, and excellent hole-expanding and bending performances at the same time. It can be used to prepare automotive structural parts, and realize the new design concept of "green-safety" for automobiles. It has good popularization prospect and application value. The annealing process according to the present disclosure plays a key role for the performances of the steel. The annealing process comprises a heating stage, a soaking stage, a slow cooling stage, a fast cooling stage, a controlled cooling stage for self-temperature rise, and an air cooling stage. By designing the process appropriately and controlling relevant process parameters, the GPa-grade bainite steel having an ultra-high yield ratio can be obtained. Correspondingly, the manufacturing method according to the present disclosure employs a unique production process. Particularly, the above annealing process is utilized to guarantee the performances of the resulting GPa-grade bainite steel. The resulting GPa-grade bainite steel not only has ultra-high strength and yield ratio, but also has excellent hole-expanding and bending performances.
Description of the Drawings Fig. 1 is a photograph at 3000x magnification showing the microstructure of the GPa-grade bainite steel of Example 1. Fig. 2 is a photograph at 3000x magnification showing the microstructure of the comparative steel in Comparative Example 7. Fig. 3 is a photograph at 1000x magnification showing the microstructure of the comparative steel in Comparative Example 8.
Detailed Description The GPa-grade bainite steel having an ultra-high yield ratio according to the present disclosure and the manufacturing method for the same will be further explained and illustrated with reference to the accompanying drawings of the specification and the specific Examples. Nonetheless, the explanation and illustration are not intended to unduly limit the technical solution of the present disclosure. Examples 1-14 and Comparative Examples 1-10 The GPa-grade bainite steel having an ultra-high yield ratio in each of Examples 1-14 was prepared using the following steps: (1) Subjecting the chemical composition shown in Table 1 to smelting and casting. (2) Hot rolling: the heating temperature was controlled at 1150-1260°C; the initial temperature of the finishing rolling was controlled at 1100-1220°C; and the final rolling temperature of the finishing rolling was controlled at 900-950°C. (3) Post-rolling cooling and coiling: the cooling rate was controlled at 30-150 °C/s; and the coiling temperature was controlled at 450-580 °C. (4) Pickling and cold rolling: the cold rolling reduction rate was controlled at > 50%. (5) Annealing. It should be noted that in step (5), the annealing process comprises the following steps: (a) Heating to a soaking temperature Ts at a heating rate of <50°C/s at a heating stage, wherein Ts was 840-900 °C; (b) Holding the temperature Ts for 5 minutes or less at a soaking stage; (c) Cooling to (Ts-80) to (Ts-140) °C at a first cooling rate of <15°C/s at a slow cooling stage; (d) Cooling to (Ts-490) to (Ts-440) °C at a second cooling rate of>(130-Q)°C/s at a fast cooling stage, wherein Q=Cx180+Six10+Mnx30+Nix50+Crx 15+Mox 15+Bx2000; (e) Cooling at a third cooling rate for 10-40 s at a controlled cooling stage for self-temperature rise, wherein [(Q-80)/12]<third cooling rate<[(Q-80)/8]; (f) Finally, cooling the strip steel in air to room temperature at an air-cooling stage. In addition, it should be noted that the GPa-grade bainite steel having an ultra-high yield ratio in each of Examples 1-14 according to the present disclosure was prepared using the above steps. The chemical compositions and related process parameters in these Examples all met the control requirements of the design specification according to the present disclosure. The comparative steel in each of Comparative Examples 1-10 was also made by the process comprising smelting and casting, hot rolling, post-rolling cooling and coiling, pickling and cold rolling, and annealing. However, the chemical composition and the relevant process parameters in each of Comparative Examples 1-6 included parameters that failed to meet the requirements of the design according to the present disclosure. Although the chemical composition in each of Comparative Examples 7-10 met the requirements of the design according to the present disclosure, these Comparative Examples all included parameters that failed to meet the requirements of the design according to the present disclosure. Among the Examples according to the present disclosure and the Comparative Examples, Comparative Example 7 and Example 1 had the same composition of chemical elements; Comparative Example 8 and Example 2 had the same composition of chemical elements; Comparative Example 9 and Example 6 had the same composition of chemical elements; and Comparative Example 10 and Example 11 had the same composition of chemical elements. Table 1 lists the mass percentages (%) of the chemical elements in the GPa-grade bainite steel having an ultra-high yield ratio in each of Examples 1-14 and the mass percentages (%) of the chemical elements in the comparative steel in each of Comparative Examples 1-10. Table 1. (the balance is Fe and other unavoidable impurities except for P and S) Stee Chemical elements
No. C Si Mn Cr B Mo Nb Ti P S Al Cu Ni V Ce Gra Cb M
de
Ex. 1 and
Comp. A 0.16 0.45 1.75 0.3 0.002 0.19 0 0 0.0100.002 0.02 0 0 0 0 0.22 0.23
Ex. 7
Ex. 2 and
Comp. B 0.17 0.35 1.82 0.2 0.004 0.23 0 0 0.0120.003 0.03 0 0 0 0 0.26 0.22
Ex. 8
Ex. 3 C 0.13 0.5 1.68 0.25 0.004 0.16 0.03 0.03 0.013 0.001 0.01 0 0 0 0 0.20 0.24
Ex. 4 D 0.19 0.23 2 0.23 0.003 0.13 0.04 0.02 0.0110.002 0.03 0 0 0 0 0.27 0.21
Ex. 5 E 0.14 0.27 1.88 0.22 0.004 0.15 0 0 0.010 0.002 0.02 0.2 0 0 0 0.24 0.18
Ex. 6 and
Comp. F 0.17 0.22 1.71 0.3 0.004 0.25 0 0 0.008 0.001 0.03 0 0 0 0 0.24 0.27
Ex. 9
Ex. 7 G 0.16 0.43 1.56 0.21 0.002 0.15 0.02 0.08 0.009 0.001 0.04 0 0 0 0 0.20 0.26
Ex. 8 H 0.19 0.41 1.53 0.35 0.002 0.12 0.06 0.01 0.010 0.001 0.05 0 0 0 0 0.23 0.26
Ex. 9 I 0.18 0.31 1.61 0.38 0.002 0 0 0.1 0.015 0.003 0.04 0 0 0 0 0.22 0.25
Ex. 10 J 0.2 0.37 1.94 0.25 0.001 0.20 0 0.01 0.010 0.002 0.02 0 0 0.2 0 0.21 0.27
Ex. 11
and K 0.15 0.48 1.58 0 0.003 0.37 0 0 0.008 0.002 0.02 0 0 0 0 0.21 0.22 Comp.
Ex. 10
Ex. 12 L 0.22 0.46 1.35 0.16 0.004 0.31 0.04 0 0.009 0.001 0.03 0 0 0 0.2 0.27 0.27
Ex. 13 M 0.12 0.4 1.93 0.11 0.003 0.20 0 0.05 0.008 0.004 0.03 0 0.2 0 0 0.22 0.21
Ex. 14 N 0.24 0.25 1.3 0.17 0.001 0.27 0.01 0.03 0.010 0.001 0.02 0 0 0 0 0.26 0.26
Comp. 0 0.25 0.35 2.1 0.35 0.001 0.2 0 0 0.0120.001 0.02 0 0 0 0 0.31 0.26 Ex. 1
Comp. P 0.10 0.4 1.7 0.3 0.002 0.25 0 0 0.013 0.003 0.02 0 0 0 0 0.15 0.27 Ex. 2
Comp. Q 0.18 0.3 1.68 0.28 0.004 0.2 0.02 0.05 0.0110.004 0.02 0 0 0 0 0.24 0.29 Ex. 3
Comp. R 0.17 0.22 1.96 0.2 0.001 0.13 0 0 0.014 0.002 0.02 0 0 0 0 0.25 0.16 Ex. 4
Comp. S 0.15 0.22 1.51 0.22 0.001 0.3 0 0 0.015 0.002 0.02 0.2 0 0 0 0.18 0.26 Ex. 5
Comp. T 0.19 0.22 1.86 0.3 0.004 0.16 0 0.01 0.012 0.003 0.02 0 0 0 0 0.28 0.22 Ex. 6
Note: in the above table, Cb=C-(Mo+Nb)/8-(Ti+V)/4-Cr/12+Ni/10+Mn/20+Bx10, wherein each element in the formula represents the value in front of the percent sign in the mass percentage of the element; M=Cr/2.5+Ti+V/5+Nb/1.7+Mo/1.7, wherein Cr, V, Nb, Ti and Mo each represent the value in front of the percent sign in the mass percentage of the chemical element.
Table 2-1 and Table 2-2 list the specific process parameters for the GPa-grade bainite steel having an ultra-high yield ratio in each of Examples 1-14 and the comparative steel in each of Comparative Examples 1-10. Table 2-1 Step (2) Step (3) Step (4)
Initial rolling Final rolling Steel Heating Coiling Cold rolling No. temperature of temperature of Cooling rate grade temperature temperature reduction rate finishing finishing (°C/s) (°C) (°C) (%) rolling (°C) rolling (°C)
Ex.1 A 1180 1140 920 70 500 50
Ex.2 B 1205 1165 945 100 525 55
Ex.3 C 1210 1170 950 50 570 80
Ex.4 D 1190 1150 930 90 480 65
Ex.5 E 1155 1115 900 100 450 70
Ex.6 F 1190 1150 930 110 510 60
Ex.7 G 1240 1200 905 40 535 75
Ex.8 H 1230 1190 910 30 580 55
Ex.9 1 1255 1215 915 150 470 60
Ex.10 J 1195 1155 935 120 515 65
Ex.11 K 1205 1165 900 100 525 55
Ex.12 L 1175 1135 915 140 495 50
Ex.13 M 1230 1190 905 130 550 60
Ex.14 N 1240 1200 950 150 460 65
Comp. Ex. 1 0 1170 1130 910 50 490 50
Comp. Ex. 2 P 1225 1185 915 100 545 70
Comp. Ex. 3 Q 1235 1195 925 120 495 65
Comp. Ex. 4 R 1215 1175 920 100 535 60
Comp. Ex. 5 S 1235 1195 900 80 505 55
Comp. Ex. 6 T 1230 1190 910 90 550 50
Comp. Ex. 7 A 1180 1140 920 70 500 70
Comp. Ex. 8 B 1205 1165 945 110 525 55
Comp. Ex. 9 F 1190 1150 930 90 510 60
Comp. Ex. K 1205 1165 900 100 525 60 10
Table 2-2 Step (5)
Step (a) Step (b) Step (c) Step (d) Step (e)
Cooling time Cooling Cooling Heating Soaking at controlled First temperature Second temperature Third No. rate at Soaking time at Self- cooling stage cooling at slow cooling at fast cooling heating temperature soaking Q temperature for self rate cooling rate cooling rate stage (°C) stage rise (°C) temperature (°C/s) stage (°C/s) stage (°C/s) (°C/s) (min) rise (°C) (°C)
Ex. 1 5 850 2.0 5 740 55 97 365 2 108 10
Ex. 2 15 860 3.0 8 730 50 103 382 2 119 34
Ex. 3 45 900 4.5 10 775 45 93 410 1 65 40
Ex. 4 10 840 1.5 7 755 55 108 390 2.5 120 22
Ex.5 20 865 1.5 12 737 50 98 385 2 100 23
Ex. 6 5 855 3.5 11 741 50 100 382 2 112 22
Ex. 7 20 875 2.5 4 762 60 89 397 1 58 30
Ex. 8 35 893 4.0 15 755 35 95 405 1.5 65 28
Ex. 9 30 862 1.5 13 725 45 94 400 1.5 51 14
Ex. 10 10 846 2.0 10 735 45 107 405 2.5 115 30
Ex. 11 15 868 1.0 8 746 50 91 380 1 80 20
Ex. 12 40 887 2.5 7 750 40 100 400 2 98 25
Ex. 13 25 858 3.0 7 725 45 104 379 2.5 98 12
Ex. 14 20 880 2.5 5 745 55 93 393 1.5 92 36
Comp. 30 860 2.5 5 740 25 122 391 4.5 123 12 Ex.1
Comp. 25 863 3.0 8 745 45 85 386 1 64 20 Ex.2
Comp. 10 858 2.0 7 735 40 101 396 2.5 111 18 Ex.3
Comp. 15 866 1.5 10 733 42 99 382 3.5 83 10 Ex.4
Comp. 5 854 2.0 15 720 50 84 378 1 71 30 Ex.5
Comp. 20 857 2.5 10 725 30 107 393 3 111 25 Ex.6
Comp. 5 852 4.0 7 740 20 97 405 2 48 10 Ex.7
Comp. 35 860 3.5 8 730 30 103 450 2.5 45 10 Ex.8
Comp. 40 855 3.0 5 741 35 100 382 1 112 10 Ex.9
Comp. 30 868 1.5 10 746 45 91 380 3 80 20 Ex. 10
Note: in the above table, Q=Cx180+Six10+Mnx30+Nix50+Crx15+Mox15+Bx2000, wherein each element in the formula represents the value in front of the percent sign in the mass percentage of the element.
Relevant mechanical performance tests were performed on the GPa-grade bainite steel having an ultra-high yield ratio in each of Examples 1-14 and the comparative steel in each of Comparative Example 1-10. The mechanical performance test results of the Examples and Comparative Examples are listed in Table 3. The relevant performance test methods are described as follows. The resulting GPa-grade bainite steel having an ultra-high yield ratio in each of Examples1 14 and the comparative steel in each of Comparative Example 1-10 were sampled respectively. A transverse JIS 5# tensile sample was used to determine the yield strength and tensile strength of the steel, and the middle area of the sheet was used to determine the hole expansion rate and bending performance of the steel. The hole expansion rate of the steel was determined in a hole expanding test, wherein a test piece with a hole in the center was pressed into a die with a punch to expand the central hole of the test piece until the edge of the hole in the plate necked or through-plate cracks appeared. Since the manner for preparing the original hole in the center of the test piece and the quality of the corresponding edge of the original hole have a great influence on the test result of the hole expansion rate, the test and test method were implemented according to the test method of hole expansion rate specified in the ISO/DIS 16630 standard. The original hole in the center was in the form of a punched hole (corresponding to the processing method for an original hole having the worst edge quality). The 1800 bending test was implemented using the method for determining bending performance in the GB/T232-2010 standard (bending diameter d=la). Table 3 lists the test results of the mechanical performances of the GPa-grade bainite steel having an ultra-high yield ratio in each of Examples 1-14 and the comparative steel in each of Comparative Examples 1-10. Table 3 Mechanical performances
No. Yield strength Tensile strength Yield Elongation Hole expansion rate 1800 bending (MPa) (MPa) ratio (%) (%)
d=1a Ex. 1 959 1003 0.96 9.3 68.2 qualified
d=1a Ex. 2 933 1022 0.91 9.7 62.2 qualified d=1a Ex. 3 927 1010 0.92 9.8 62 qualified d=1a Ex. 4 936 1038 0.90 9.6 56.7 qualified d=1a Ex. 5 918 1019 0.90 10.5 58.4 qualified d=1a Ex. 6 966 1031 0.94 9.5 65.4 qualified d=1a Ex. 7 924 1016 0.91 9.6 61.3 qualified d=1a Ex. 8 922 1026 0.90 10.5 61.8 qualified d=1a Ex. 9 915 1015 0.90 11 55.5 qualified d=1a Ex. 10 948 1020 0.93 9.7 61 qualified d=1a Ex. 11 911 1008 0.90 10.7 55.9 qualified d=1a Ex. 12 942 1037 0.91 10.3 59.3 qualified d=1a Ex. 13 915 1008 0.91 10.8 57 qualified d=1a Ex. 14 941 1005 0.94 9.4 66.2 qualified
Comp. 1075 1158 0.93 7.8 44.2 d=l a cracked Ex.1
Comp. d=1a 849 942 0.90 11.2 68.8 Ex. 2 qualified
Comp. 1008 1098 0.92 8.2 51.9 d=la cracked Ex. 3
Comp. 1031 1129 0.91 8 47.7 d=la cracked Ex.4
Comp. d=1a 875 977 0.90 10.8 66.9 Ex. 5 qualified
Comp. 1020 1147 0.89 8.9 50.3 d=la cracked Ex. 6
Comp. 802 999 0.80 11.9 43.9 d=l a cracked Ex. 7
Comp. 781 996 0.78 12.4 40.1 d=l a cracked Ex. 8
Comp. 974 1035 0.94 8.8 52.2 d=la cracked Ex. 9
Comp. 887 1002 0.89 11.6 53.4 d=la cracked Ex. 10
As it can be seen from Table 3, as compared with the comparative steels in Comparative Examples 1-10, the mechanical performances of the GPa-grade bainite steels having an ultra-high yield ratio in Examples 1-14 according to the present disclosure are obviously better. The GPa-grade bainite steels having an ultra-high yield ratio in Examples 1-14 according to the present disclosure have an ultra-high yield ratio, an ultra-high strength and excellent hole expanding and bending performances at the same time, with a tensile strength of >980 MPa, a yield strength of > 900 MPa, a yield ratio of > 0.9, and a hole expansion rate of > 55%. In some individual preferred embodiments, as in Example 1, the GPa-grade bainite steel having an ultra-high yield ratio in Example 1 has a yield strength of > 950 MPa, and a yield ratio of > 0.95. That is, it has an ultra-high yield ratio and an ultra-high yield strength. Fig. 1 is a photograph at 3000x magnification showing the microstructure of the GPa-grade bainite steel of Example 1. As shown by Fig. 1, the microstructure of the matrix of the GPa-grade bainite steel in Example 1 is acicular lower bainite because it was cooled to the lower bainite phase region (the cooling temperature of the fast cooling met the requirement of the present disclosure) at a sufficiently fast cooling rate (the second cooling rate met the requirement of the present disclosure) at the fast cooling stage. In addition, because the cooling rate at the controlled cooling stage for self temperature rise was suitable (the third cooling rate met the requirement of the present disclosure), the structure also contains a fine nano-, submicron-ormicron-scale granular carbide precipitate phase that has been dispersively precipitated. The phase proportion of the acicular lower bainite is >90%; the total phase proportion of the granular carbide precipitate phase + the acicular lower bainite is >99%; and the maximum diameter of the granular carbide precipitate is <2 m. Fig. 2 is a photograph at 3000x magnification showing the microstructure of the comparative steel in Comparative Example 7.
As shown by Fig. 2, because the cooling rate was insufficient (the second cooling rate did not meet the requirement of the present disclosure) when the comparative steel in Comparative Example 7 was cooled at the fast cooling stage, bainite phase transformation occurred in the comparative steel at high temperature before it was cooled to the lower bainite phase region. Although it was still cooled to an appropriate temperature of the lower bainite phase region eventually, its microstructure is still dominated by massive equiaxed bainite, nearly free of acicular lower bainite, and the carbide precipitate is also not fine and uniform enough. Fig. 3 is a photograph at 1000x magnification showing the microstructure of the comparative steel in Comparative Example 8. As shown by Fig. 3, although the cooling rate was appropriate (the second cooling rate met the requirement of the present disclosure) when the comparative steel in Comparative Example 8 was cooled at the fast cooling stage, the cooling temperature of the fast cooling was too high (the cooling temperature at the fast cooling stage did not meet the requirement of the present disclosure). As a result, its microstructure almost consists of massive equiaxed bainite, nearly free of acicular lower bainite, and the carbide precipitate is also not fine and uniform enough. To sum up, as it can be seen, by designing the chemical composition appropriately according to the present disclosure, a GPa-grade bainite steel having an ultra-high yield ratio that has a tensile strength of > 980 MPa, a yield strength of > 900 MPa, a yield ratio of > 0.9, and a hole expansion rate of > 55% can be obtained. The GPa-grade bainite steel has an ultra-high yield ratio, an ultra high strength, and excellent hole-expanding and bending performances at the same time. It can be used to prepare automotive structural parts, and realize the new design concept of "green-safety" for automobiles. It has good popularization prospect and application value. The annealing process according to the present disclosure plays a key role for the performances of the steel. The annealing process comprises a heating stage, a soaking stage, a slow cooling stage, a fast cooling stage, a controlled cooling stage for self-temperature rise, and an air cooling stage. By designing the process appropriately and controlling relevant process parameters, the GPa-grade bainite steel having an ultra-high yield ratio can be obtained. Correspondingly, the manufacturing method according to the present disclosure employs a unique production process. Particularly, the above annealing process is utilized to guarantee the performances of the resulting GPa-grade bainite steel. The resulting GPa-grade bainite steel not only has ultra-high strength and yield ratio, but also has excellent hole-expanding and bending performances. In addition, the ways in which the various technical features of the present disclosure are combined are not limited to the ways recited in the claims of the present disclosure or the ways described in the specific examples. All the technical features recited in the present disclosure may be combined or integrated freely in any manner, unless contradictions are resulted. It should also be noted that the Examples set forth above are only specific examples according to the present disclosure. Obviously, the present disclosure is not limited to the above Examples. Similar variations or modifications made thereto can be directly derived or easily contemplated from the present disclosure by those skilled in the art. They all fall in the protection scope of the present disclosure.
Claims (15)
- What is claimed is: 1. A GPa-grade bainite steel having an ultra-high yield ratio, comprising the following chemical elements in mass percentages in addition to Fe and unavoidable impurities: C: 0.12-0.24%; Si: 0.2-0.5%; Mn: 1.3-2.0%; B: 0.001-0.004%; Al: 0.01-0.05%; at least one of Cr, Nb, Ti and Mo, wherein Cr<0.4%, Nb0.06%, Ti<O.1%, Mo<0.4%.
- 2. The GPa-grade bainite steel having an ultra-high yield ratio according to claim 1, wherein the mass percentages of the chemical element are: C: 0.12-0.24%; Si: 0.2-0.5%; Mn: 1.3-2.0%; B: 0.001-0.004%; Al: 0.01-0.05%; at least one of Cr, Nb, Ti and Mo, wherein Cr<0.4%, Nb0.06%, Ti0.1%, Mo<0.4%; a balance of Fe and other unavoidable impurities.
- 3. The GPa-grade bainite steel having an ultra-high yield ratio according to claim 1 or 2, wherein the mass percentages of the chemical elements satisfy at least one of: C: 0.15-0.20%, Mn: 1.6-2.0%.
- 4. The GPa-grade bainite steel having an ultra-high yield ratio according to claim 1 or 2, wherein among the other unavoidable impurities: P < 0.015%; and/or S < 0.004%.
- 5. The GPa-grade bainite steel having an ultra-high yield ratio according to claim 1 or 2, further comprising at least one of the following chemical elements: 0<Cus0.2%, 0<Ni<0.2%, 0<V<0.2%, 0<Ce<0.2%.
- 6. The GPa-grade bainite steel having an ultra-high yield ratio according to claim 5, wherein it satisfies 0.18<M<0.27, wherein M=Cr/2.5+Ti+V/5+Nb/1.7+Mo/1.7, wherein Cr, V, Nb, Ti and Mo each represent a value in front of a percent sign in the mass percentage of each chemical element; and/or 0.20<Cb<0.27, wherein an equivalent bainite carbon content C=C (Mo+Nb)/8-(Ti+V)/4-Cr/12+Ni/10+Mn/20+Bx10, wherein each element in the above formula represents a value in front of a percent sign in the mass percentage of the element.
- 7. The GPa-grade bainite steel having an ultra-high yield ratio according to claim 1 or 2, wherein its microstructure is mainly acicular lower bainite, and a phase proportion of the acicular lower bainite is > 90%.
- 8. The GPa-grade bainite steel having an ultra-high yield ratio according to claim 7, wherein its microstructure further comprises a nano-, submicron- or micron-scale granular carbide precipitate phase that is precipitated dispersively, and a total phase proportion of the granular carbide precipitate phase + acicular lower bainite is >99%; preferably, the granular carbide precipitate has a maximum diameter of <2 m.
- 9. The GPa-grade bainite steel having an ultra-high yield ratio according to claim 1, wherein it has a tensile strength of >980 MPa, a yield strength of >900 MPa, a yield ratio of >0.9, and a hole expansion rate of > 55%; preferably a yield strength of >950 MPa, and a yield ratio of >0.95.
- 10. An annealing process for the GPa-grade bainite steel having an ultra-high yield ratio according to any one of claims 1-9, comprising steps of: (a) Heating a strip steel to a soaking temperature Ts at a heating rate of <50°C/s at a heating stage, wherein Ts is 840-900 °C; (b) Holding the temperature Ts for 5 minutes or less at a soaking stage; (c) Cooling to (Ts-80) to (Ts-140) °C at a first cooling rate of <15°C/s at a slow cooling stage; (d) Cooling to (Ts-490) to (Ts-440) °C at a second cooling rate of >(130-Q)°C/s at a fast cooling stage; (e) Cooling at a third cooling rate for 10-40 s at a controlled cooling stage for self temperature rise, wherein [(Q-80)/12]<third cooling rate<[(Q-80)/8]; (f) Finally, cooling the strip steel in air to room temperature at an air-cooling stage; wherein Q=Cx180+Six1O+Mnx3O+Nix5O+Crx15+Mox15+Bx2000.
- 11. A manufacturing method for a GPa-grade bainite steel having an ultra-high yield ratio, comprising steps of: (1) Smelting and casting; (2) Hot rolling; (3) Post-rolling cooling and coiling; (4) Pickling and cold rolling. (5) The annealing process according to claim 10.
- 12. The manufacturing method according to claim 11, wherein in the step (2), a heating temperature is controlled at 1150-1260 °C; an initial rolling temperature of finishing rolling is controlled at 1100-1220 °C; and a final rolling temperature of finishing rolling is controlled at 900-950 °C.
- 13. The manufacturing method according to claim 11, wherein in step (3), a cooling rate is controlled at 30-150 °C/s, and a coiling temperature is controlled at 450-580 °C.
- 14. The manufacturing method according to claim 11, wherein in step (4), a cold rolling reduction rate is controlled at > 50%.
- 15. The manufacturing method according to claim 11, wherein the GPa-grade bainite steel having an ultra-high yield ratio is the GPa-grade bainite steel having an ultra-high yield ratio according to any one of claims 1-9.EXPERIENCE Exp= -491 IA-49 VID= IND=Fig. 1 Fig. 1Type on en = seen 8000 N No hage SOLEX Non- SOLK - IR.E WITH no=Fig. 22 Fig.1/2 1/2 épic an = 1000 RE Meg to NO no= no= Room FT = Deg termsFig. 3 Fig. 32/2 2/2
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| CN202010879001.3A CN114107785B (en) | 2020-08-27 | 2020-08-27 | Gipa-grade bainite steel with ultrahigh yield ratio and manufacturing method thereof |
| CN202010879001.3 | 2020-08-27 | ||
| PCT/CN2021/114658 WO2022042622A1 (en) | 2020-08-27 | 2021-08-26 | Gpa-grade bainite steel having ultra-high yield ratio and manufacturing method for gpa-grade bainite steel |
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| EP (1) | EP4206347A4 (en) |
| JP (1) | JP2023538680A (en) |
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| CN (1) | CN114107785B (en) |
| AU (1) | AU2021332868A1 (en) |
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| CN115896608B (en) * | 2021-09-30 | 2024-07-12 | 宝山钢铁股份有限公司 | Bainite steel and preparation method thereof |
| CN116926412A (en) * | 2022-03-29 | 2023-10-24 | 宝山钢铁股份有限公司 | Bainite seamless steel tube and manufacturing method thereof |
| CN114908291B (en) * | 2022-04-27 | 2023-04-14 | 鞍钢股份有限公司 | 850 MPa-level precipitation strengthening type hot-rolled bainite steel and production method thereof |
| CN114892080B (en) * | 2022-04-27 | 2023-06-20 | 鞍钢股份有限公司 | 720 MPa-grade precipitation-strengthening type hot rolled bainitic steel and production method thereof |
| CN114908290B (en) * | 2022-04-27 | 2023-04-14 | 鞍钢股份有限公司 | 520 MPa-grade precipitation strengthening hot-rolled bainite steel and production method thereof |
| CN115386693B (en) * | 2022-08-18 | 2023-07-25 | 马鞍山钢铁股份有限公司 | Continuous annealing method for cold-rolled dual-phase steel with 590 MPa-level tensile strength |
| CN115354237B (en) * | 2022-08-29 | 2023-11-14 | 东北大学 | Hot-rolled ultrahigh-strength steel plate with tensile strength of 1000MPa and preparation method thereof |
| CN115323275B (en) * | 2022-09-05 | 2023-07-04 | 东北大学 | High-strength high-toughness rare earth warm-rolled low-carbon low-manganese TRIP steel and preparation method thereof |
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| JPH05287439A (en) * | 1992-04-07 | 1993-11-02 | Nippon Steel Corp | Mo-v type ultrahigh tensile strength resistance welded steel tube excellent in ductility |
| CN100343408C (en) * | 2004-12-08 | 2007-10-17 | 鞍钢股份有限公司 | Bainite steel with high tensile strength, high toughness and low yield ratio and production method thereof |
| CN101008066B (en) * | 2006-01-27 | 2010-05-12 | 宝山钢铁股份有限公司 | Hot rolling martensite steel plate with tensile strength higher than 1000Mpa and its production method |
| JP2008156680A (en) * | 2006-12-21 | 2008-07-10 | Nippon Steel Corp | High-strength cold rolled steel sheet having high yield ratio, and its production method |
| KR100925639B1 (en) | 2007-12-24 | 2009-11-06 | 주식회사 포스코 | High strength cold-rolled steel sheet having excellent weather resistance and method manufacturing the Same |
| CN102337482B (en) * | 2010-07-23 | 2013-11-20 | 宝山钢铁股份有限公司 | Bainite high strength and toughness steel plate with yield strength of 900 MPa and manufacture method thereof |
| US9115416B2 (en) * | 2011-12-19 | 2015-08-25 | Kobe Steel, Ltd. | High-yield-ratio and high-strength steel sheet excellent in workability |
| JP5860333B2 (en) | 2012-03-30 | 2016-02-16 | 株式会社神戸製鋼所 | High yield ratio high strength cold-rolled steel sheet with excellent workability |
| CN102719736B (en) | 2012-06-12 | 2014-07-09 | 武汉钢铁(集团)公司 | Steel with yield ratio of 0.9 or more used for ultra-fine grain slideway and production method thereof |
| MX2015014437A (en) * | 2013-04-15 | 2016-02-03 | Jfe Steel Corp | High strength hot rolled steel sheet and method for producing same. |
| CN103233183B (en) * | 2013-04-18 | 2016-03-30 | 南京钢铁股份有限公司 | A kind of yield strength 960MPa grade super strength steel plate and manufacture method thereof |
| KR101518600B1 (en) * | 2013-10-23 | 2015-05-07 | 주식회사 포스코 | Ultrahigh strength hot rolled steel sheet having excellent impact resistant property and manufacturing mehtod the same |
| KR101910444B1 (en) * | 2014-02-27 | 2018-10-22 | 제이에프이 스틸 가부시키가이샤 | High-strength hot-rolled steel sheet and method for manufacturing the same |
| JP6056790B2 (en) * | 2014-02-27 | 2017-01-11 | Ｊｆｅスチール株式会社 | High strength hot rolled steel sheet and method for producing the same |
| US10435762B2 (en) | 2014-03-31 | 2019-10-08 | Jfe Steel Corporation | High-yield-ratio high-strength cold-rolled steel sheet and method of producing the same |
| JP6252692B2 (en) * | 2015-07-27 | 2017-12-27 | Ｊｆｅスチール株式会社 | High strength hot rolled steel sheet and method for producing the same |
| US20210140007A1 (en) * | 2018-07-31 | 2021-05-13 | Jfe Steel Corporation | High-strength hot rolled steel sheet and method for manufacturing same |
| CN109988969B (en) * | 2019-04-01 | 2021-09-14 | 山东钢铁集团日照有限公司 | Cold-rolled Q & P1180 steel with different yield ratios and production method thereof |
| CN110747405B (en) * | 2019-10-24 | 2021-09-14 | 邯郸钢铁集团有限责任公司 | One-thousand-megapascal-grade cold-rolled bainite steel plate suitable for rolling and preparation method thereof |
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| KR20230058083A (en) | 2023-05-02 |
| US20230357882A1 (en) | 2023-11-09 |
| WO2022042622A1 (en) | 2022-03-03 |
| CN114107785A (en) | 2022-03-01 |
| JP2023538680A (en) | 2023-09-08 |
| AU2021332868A1 (en) | 2023-05-04 |
| MX2023002204A (en) | 2023-03-03 |
| CN114107785B (en) | 2022-10-21 |
| EP4206347A1 (en) | 2023-07-05 |
| EP4206347A4 (en) | 2024-03-27 |
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