CN109136737A - A kind of tensile strength 1100MPa grades of ultra-high strength and toughness steel and its manufacturing method - Google Patents
A kind of tensile strength 1100MPa grades of ultra-high strength and toughness steel and its manufacturing method Download PDFInfo
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- CN109136737A CN109136737A CN201810638000.2A CN201810638000A CN109136737A CN 109136737 A CN109136737 A CN 109136737A CN 201810638000 A CN201810638000 A CN 201810638000A CN 109136737 A CN109136737 A CN 109136737A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 135
- 239000010959 steel Substances 0.000 title claims abstract description 135
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 18
- 238000005496 tempering Methods 0.000 claims abstract description 42
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 29
- 238000010791 quenching Methods 0.000 claims abstract description 24
- 230000000171 quenching effect Effects 0.000 claims abstract description 24
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 22
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 17
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 11
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 11
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 11
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 10
- 239000000126 substance Substances 0.000 claims abstract description 10
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 9
- 230000008602 contraction Effects 0.000 claims abstract description 8
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 8
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 7
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 7
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 6
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 6
- 229910052802 copper Inorganic materials 0.000 claims abstract description 5
- 229910052739 hydrogen Inorganic materials 0.000 claims abstract description 5
- 229910052760 oxygen Inorganic materials 0.000 claims abstract description 4
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 3
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 238000010438 heat treatment Methods 0.000 claims description 28
- 230000000717 retained effect Effects 0.000 claims description 12
- 238000005242 forging Methods 0.000 claims description 7
- 241001417490 Sillaginidae Species 0.000 claims description 2
- 239000000203 mixture Substances 0.000 abstract description 2
- 238000000034 method Methods 0.000 description 19
- 238000005096 rolling process Methods 0.000 description 16
- 230000008569 process Effects 0.000 description 11
- 239000010949 copper Substances 0.000 description 10
- 238000001816 cooling Methods 0.000 description 9
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- 229910052799 carbon Inorganic materials 0.000 description 8
- 239000013078 crystal Substances 0.000 description 6
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- 230000000694 effects Effects 0.000 description 5
- PNEYBMLMFCGWSK-UHFFFAOYSA-N Alumina Chemical compound [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 4
- 238000005275 alloying Methods 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 238000010583 slow cooling Methods 0.000 description 4
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 3
- 230000008859 change Effects 0.000 description 3
- 238000009749 continuous casting Methods 0.000 description 3
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- 229910052742 iron Inorganic materials 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 238000005457 optimization Methods 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 238000005204 segregation Methods 0.000 description 3
- 239000000243 solution Substances 0.000 description 3
- 230000009466 transformation Effects 0.000 description 3
- 238000003723 Smelting Methods 0.000 description 2
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 2
- 229910000754 Wrought iron Inorganic materials 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 238000004873 anchoring Methods 0.000 description 2
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- 230000003111 delayed effect Effects 0.000 description 2
- 238000011161 development Methods 0.000 description 2
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- 125000004435 hydrogen atom Chemical group [H]* 0.000 description 2
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- 239000013535 sea water Substances 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910003286 Ni-Mn Inorganic materials 0.000 description 1
- 238000004220 aggregation Methods 0.000 description 1
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- 125000004429 atom Chemical group 0.000 description 1
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- 238000003776 cleavage reaction Methods 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- RKTYLMNFRDHKIL-UHFFFAOYSA-N copper;5,10,15,20-tetraphenylporphyrin-22,24-diide Chemical compound [Cu+2].C1=CC(C(=C2C=CC([N-]2)=C(C=2C=CC=CC=2)C=2C=CC(N=2)=C(C=2C=CC=CC=2)C2=CC=C3[N-]2)C=2C=CC=CC=2)=NC1=C3C1=CC=CC=C1 RKTYLMNFRDHKIL-UHFFFAOYSA-N 0.000 description 1
- 229910052593 corundum Inorganic materials 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
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- 238000004146 energy storage Methods 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 230000002706 hydrostatic effect Effects 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- 230000001939 inductive effect Effects 0.000 description 1
- 230000008595 infiltration Effects 0.000 description 1
- 238000001764 infiltration Methods 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 230000005764 inhibitory process Effects 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 230000002906 microbiologic effect Effects 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 239000010813 municipal solid waste Substances 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
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- 230000035939 shock Effects 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 230000001629 suppression Effects 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
- 229910001845 yogo sapphire Inorganic materials 0.000 description 1
Classifications
-
- 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
- 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
- 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
-
- 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
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
-
- 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
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- 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
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- 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
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- 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
-
- 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
- C21D2211/001—Austenite
-
- 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
-
- 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
- C21D2211/008—Martensite
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- Crystallography & Structural Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
A kind of tensile strength 1100MPa grades of ultra-high strength and toughness steel and its manufacturing method, the steel chemical composition weight percent are as follows: C:0.245~0.350%, Si:0.10~0.50%, Mn:0.20~1.20%, P≤0.015%, S≤0.003%, Cr:0.30~1.20%, Mo:0.20~0.80%, Ni:2.00~3.70%, Cu:0~0.30%, Nb:0~0.08%, V:0~0.12%, Al:0.01~0.08%, Ti:0.003~0.06%, Ca≤0.005%, H≤0.0002%, N≤0.0120%, O≤0.0030%, remaining is Fe and inevitable impurity.The present invention is heat-treated using quenching+tempering, obtains tempered martensite+tempering bainite and residual austenite body tissue.Yield strength >=900MPa of steel of the present invention, tensile strength >=1100MPa, Xia Shi Impact energy Ak v (- 20 DEG C) >=70J, elongation percentage >=15%, the contraction percentage of area >=50%, with good intensity, low-temperature flexibility and plasticity, it can be used for manufacturing high-performance marine platform mooring cable of R6 grade etc..
Description
Technical field
The present invention relates to the superhigh intensity steels with good low-temperature toughness, and in particular to a kind of tensile strength 1100MPa
Grade ultra-high strength and toughness steel and its manufacturing method.
Background technique
Production and high security machinery and structure base part of the high strength steel bar applied to ocean platform mooring cable.With
The marine resources development at deep-sea, ocean platform enlargement, structure and function complicate, requirement to ocean platform mooring cable also day
Benefit improves.The use environment of ocean platform mooring cable is severe, bears sea washes, seawater when high tensile load, ocean wave motion
Corrode the influence with microbiologic(al) corrosion.Ocean platform mooring chain steel mainly includes R3, R3S, R4, R4S, R5 etc. at present.It is corresponding
Tensile strength be 690MPa, 770MPa, 860MPa, 960MPa and 1000MPa respectively.Offshore Platform needs higher intensity
The mooring chain steel of rank and more high impact toughness.
There is more research to high strength steel material both at home and abroad, usually choose chemical component appropriate, using controlled rolling control
Refrigeration is but or Q-tempering technique, production meet the high strength steel material of mechanical property requirements.Height is produced using controlled rolling and controlled cooling mode
Intensity steel, control difficulty is larger in rolling and cooling procedure, influences the whole uniformity of steel mechanical property.Using quenching back
Fire process production high strength steel improves the harden ability of steel, makes steel in cooling by the content of optimized alloy element and carbon
Martensitic structure is formed in the process.Martensite is that carbon is solid-solubilized in iron atom body-centered cubic lattic, makes bcc lattice along c-axis direction
The tetragonal extended to form, such tissue intensity with higher and hardness.High strength steel based on martensite, by
Reach 1000J/mol in strain energy storage, dislocation density is big, causes low-temperature impact work poor.In martensite type high intensity steel grade
There are high density dislocations and sub boundary in portion, occur that mistake can be broken rapidly in the case where tiny flaw such as micro-crack during stretching
Effect, elongation percentage are lower.The Recent Progresses In The Development of requirement and current high tough product in conjunction with ocean platform to mooring cable, need to develop has
More preferable obdurability matching, excellent extension property steel.
Chinese patent CN103667953A discloses a kind of low environment crack sensitivity ultra-high strength and toughness mooring chain steel, the steel
Middle C:0.12~0.24%, Mn:0.10~0.55%, Si:0.15~0.35%, Cr:0.60~3.50%, Mo:0.35~
0.75%, N≤0.006%, Ni:0.40~4.50%, Cu≤0.50%, S≤0.005%, P:0.005~0.025%, O≤
0.0015%, H≤0.00015%, using mentioned component and the high tough mooring chain steel of quenching technical production twice, tensile strength
>=1110MPa, yield tensile ratio 0.88~0.92, elongation percentage >=12%, the contraction percentage of area >=50%, -20 DEG C of ballistic work (Akv) >=
50J.But the microstructure of the steel is upper bainite+lower bainite+martensite, upper bainite+lower bainite.
Summary of the invention
The purpose of the present invention is to provide a kind of tensile strength 1100MPa grades of ultra-high strength and toughness steel and its manufacturing method, the steel
Tensile strength reach 1100MPa grades, while there is good low-temperature flexibility and elongation percentage, can be used for ocean platform mooring
Chain, automobile and mechanical structure etc. need the occasion of high strength steel.
In order to achieve the above objectives, the technical scheme is that
A kind of tensile strength 1100MPa grades of ultra-high strength and toughness steel, chemical component weight percentage includes: C:0.245~
0.350%, Si:0.10~0.50%, Mn:0.20~1.20%, P≤0.015%, S≤0.003%, Cr:0.30~
1.20%, Mo:0.20~0.80%, Ni:2.00~3.70%, Cu:0~0.30%, Nb:0~0.08%, V:0~0.12%,
Al:0.01~0.08%, Ti:0.003~0.06%, Ca≤0.005%, H≤0.0002%, N≤0.0120%, O≤
0.0030%, remaining is Fe and inevitable impurity.
Further, the microstructure of the tensile strength 1100MPa grades of ultra-high strength and toughness steel is tempered martensite+tempering bayesian
Body and residual austenite body tissue.
Yield strength >=900MPa of tensile strength 1100MPa grades of ultra-high strength and toughness steel of the present invention, tensile strength >=
1100MPa, Xia Shi Impact energy Ak v (- 20 DEG C) >=70J, elongation percentage >=15%, the contraction percentage of area >=50%.
In the ingredient design of steel of the present invention:
C:C is added to the harden ability that steel are improved in steel, and steel is made to form the higher low temperature of hardness in quenching cooling procedure
Phase-change organization.C content improves, then can improve the hard mutually such as ratio of martensitic phase and lower bainite phase, improve the hardness of steel, but
It will lead to toughness decline.C content is too low, will lead to low temperature phase change tissue such as martensite and lower bainite content is low, can not obtain
Higher tensile strength.Therefore, it is 0.245~0.350% that the present invention, which controls C content,.
Si:Si substitutes Fe atom in steel with substitute mode, hinders dislocation motion, is beneficial to steel strength promotion.Si can
C is reduced in ferritic middle diffusivity, therefore suitable Si can avoid being formed coarse carbide in fault location in tempering
It is precipitated.But higher Si content can reduce the low-temperature impact toughness of steel.Therefore, the present invention in control Si content be 0.10~
0.50%.
Mn:Mn is retained austenite stabilizing element, and the Mn in steel mainly exists with solution.Steel is in quenching process
In, Mn can inhibit diffusion transformation, improve the harden ability of steel, form low temperature phase change tissue, this class loading intensity with higher.
But Mn too high levels will lead to form more retained austenite, reduce the yield strength of steel.Therefore, it is added in the present invention
0.20~1.20% Mn is conducive to the harden ability for improving steel, avoids the formation of more retained austenite.
P: P can reduce the combination energy of crystal boundary, deteriorate the low temperature impact properties of steel in crystal boundary segregation in steel.P and Mn are deposited jointly
It can aggravate steel belt roof bolt brittleness.Grain boundary fracture, shape occurs when the P of crystal boundary segregation can make steel in the effect by shock loading
At biggish cleavage surface, the energy that steel is absorbed when being impacted is reduced.The P no more than 0.015% is added in the present invention, guarantees
The low-temperature impact toughness of unimach.
Solubility very little of the S:S in delta ferrite and austenite, during solidification of molten steel, segregation can occur for S, be formed
More sulphide inculsion endangers the ultrasonic examination performance and low temperature impact properties of steel.S is added in Cutting free steel grade to be formed
CaS promotes cutting ability.The principal element that steel grade of the present invention considers the control of S content is that coarse sulfide is avoided to liquidate
Hit performance compromise.Therefore, the S no more than 0.003% is added in the present invention, guarantees that steel have good low temperature impact properties.
Cr:Cr is added in steel, can inhibit the diffusion transformation of steel, improves the harden ability of steel, forms the martensite of hardening
Tissue obtains the steel with higher-strength.Simultaneously in heating process, if the carbide of Cr is not completely dissolved, suppression is played
The effect of Austenite Grain Growth processed.But Cr too high levels will form coarse carbide, impaired low temperature impact performance.Therefore,
0.30~1.20% Cr is added in the present invention, guarantees the intensity and low temperature impact properties of steel.
Mo:Mo is ferrite former, conducive to improve steel harden ability, make steel is formed in quenching process bainite with
Martensite.If quenching velocity is very fast, and is tempered in lower temperature range, then Mo is mainly present in steel with solution, is risen
It to solid solution strengthening effect, is tempered in higher temperature, will form the intensity that tiny carbide improves steel.Mo is precious alloy member
Element, higher Mo, which is added, will lead to cost increase.Therefore, 0.20~0.80% Mo is added in the present invention, to obtain obdurability
With the matching of welding performance.
Nb:Nb is added in steel, plays the inhibiting effect to steel recrystallization, recrystallizes steel in lower temperature, refines Ovshinsky
Body, to achieve the purpose that refinement is finally organized.Nb content is higher, will form coarse NbC particle under high temperature tempered condition,
Deteriorate steel low-temperature impact work.Cooperate other alloying elements, 0~0.08% Nb is added in the present invention to guarantee the mechanical property of steel
Energy.
Ni:Ni exists in steel with solution, and in component system of the invention, Ni is deposited with the FCC phase of Fe-Ni-Mn
Stacking fault energy is being reduced, the low temperature impact properties of steel are improved.Ni is austenitizing formation element, and excessively high Ni content will lead to steel
Residual austenite content in material is excessively high, reduces the intensity of steel, and 2.00~3.70% Ni therefore, in the present invention is added, to protect
Demonstrate,prove the low-temperature impact toughness and intensity of steel.
Cu:Cu is added in steel, can be formed subtle nanoscale ε-Cu in drawing process and is precipitated, improve the strong of steel
Degree, while the corrosion resistance that a certain amount of Cu is conducive to improve steel is added, but since the fusing point of Cu is lower, if Cu contains
Measure it is excessively high, heating austenitization in copper can be enriched in crystal boundary, lead to grain-boundary weakness thus cracking.Therefore, in the present invention
Cu content is no more than 0.30%.
V:V and C forms VC, and tiny VC can play certain inhibition to dislocation, improve the intensity of steel.Higher temperature
Under conditions of tempering, it if C and V content are higher, will form coarse VC particle, reduce the impact property of steel, the present invention
0~0.12% V is added to guarantee the mechanical property of steel in the middle other alloying elements of combination.
Al:Al forms tiny AlN in steel-making and is precipitated, and inhibits Austenite Grain Growth in subsequent cooling procedure,
Achieve the purpose that fining austenite grains, improve the toughness of steel at low temperature.The excessively high oxidation that will lead to biggish Al of Al content
Object is formed, and steel ultrasonic examination is not conformed to.Coarse aluminium oxide hard inclusions can deteriorate the fatigue behaviour of steel.Therefore, of the invention
The Al of middle addition 0.01~0.08% improves the toughness of steel.
Ti:Ti and C and N formation compound in steel, the formation temperature of TiN is 1400 DEG C or more, usually in liquid phase or δ iron
It is precipitated in ferritic, realizes the purpose of fining austenite grains.Ti too high levels will form coarse TiN and be precipitated, lead to rushing for steel
Hitting performance and fatigue behaviour reduces.In drawing process, if Ti too high levels, the increase of low-temperature impact work fluctuating range will lead to.
Therefore, the Ti content in the present invention is controlled 0.003~0.06%.
Ca: suitable Ca element is added in steel, can form CaS, improves the size and shape of field trash, improves steel
Low-temperature impact toughness, therefore, Ca content control below 0.005%.
Effect of the H:H by the edge dislocation hydrostatic pressing field of force in steel can be assembled in fault location, form hydrogen embrittlement.Tensile strength
In rank 1100MPa and the above steel, dislocation, sub boundary isodensity are high, if H content is excessively high, then in steel quenching and tempering heat treatment
Afterwards, fault location is enriched with more H atom.H atom aggregation will form H molecule, cause steel that delayed fracture occurs.If using H is contained
Higher bar production ocean platform mooring cable is measured, since seawater is to the corrosion of mooring cable and the infiltration of H, will lead to high-intensitive system
Delayed fracture occurs when in use for pool chain, jeopardizes the safety of ocean platform.Therefore, H content control is being no more than in the present invention
0.0002%.
N, O:N form AlN or TiN in steel grade, play the role of fining austenite grains, but N content increase will lead to it
Increase in fault location enriching quantity, is formed simultaneously coarse nitride and particle is precipitated, influence steel low-temperature impact work, therefore N content control
System is being no more than≤0.0120%.The Al of O and steel grade forms Al2O3, TiO etc., to guarantee structure of steel uniformity and low-temperature impact
Function, O content are no more than 0.0030%.
The manufacturing method of tensile strength 1100MPa grades of ultra-high strength and toughness steel of the present invention comprising following steps:
1) it smelts, cast
It smelted, cast according to above-mentioned chemical component；
2) it heats
Heating temperature is 1050~1250 DEG C；
3) it rolls or forges
Finishing temperature >=760 DEG C or final forging temperature >=760 DEG C；
4) quenching heat treatment
Hardening heat is 840~1050 DEG C；
5) tempering heat treatment
Tempering temperature is 500~650 DEG C, air-cooled after tempering.
Steel of the present invention heats austenitizing under the conditions of 1050~1250 DEG C.In heating process, the carbon of Nb, V and Ti are nitrogenized
Object, Cr and Mo carbide portion or be fully dissolved in austenite, in subsequent rolling/forging and cooling procedure, Nb, V
Tiny carbonitride, anchoring austenite grain boundary are formed with Ti, refinement steel rolls state tissue.The Cr and Mo being solid-solubilized in austenite,
Improve the harden ability of steel.The Cr and Mo being solid-solubilized in austenite improve the hardenability of martensite in quenching.
Under conditions of finishing temperature or final forging temperature >=760 DEG C, recrystallization and strain inducing occur steel of the present invention for steel
Be precipitated etc., the bainite and martensite complex phase matrix with retained austenite, refinement is formed, and have tiny carbonitride
It is precipitated.
It is quenched after being heated to 840~1050 DEG C of heat preservations after steel rolling of the present invention or forging.It is quenched in heating process,
The carbonitride of carbide former Nb, V, Ti, Cr and Mo completely or partially dissolve.Undissolved carbonitride anchoring Ovshinsky
Body crystal boundary avoids austenite grain excessively coarse, realizes the purpose of crystal grain refinement after quenching, improves the obdurability of steel.It is quenching
In cooling procedure, the alloying element being solid-solubilized in austenite improves the harden ability of steel, so that final martensite is more tiny, it is such
Tissue has superhigh intensity and good toughness.
The quenched steel of the present invention is in 500~650 DEG C of progress tempering heat treatments.In quenching process, steel is formed the present invention
There are biggish strain storage energy, internal stress in retained austenite and the biggish lower bainite of defect concentration and martensitic structure, inside
It is unevenly distributed.During next high tempering, Nb, V meeting and C, N form tiny carbide, while Cr and Mo exist
Tiny Carbide Precipitation is also formed during high tempering, improves the intensity and obdurability matching of steel.Simultaneously because highly dense
Degree dislocation is buried in oblivion to be moved with low angle boundary, keeps the microstructure of steel more uniform, improves after lonneal that elongation percentage is low to be showed
As.In tempering range of the present invention, it is ensured that steel has good obdurability and strong plasticity, and the interior of steel is effectively reduced
Portion's stress is conducive to the processing and use of bar, such as produces high performance R6 ocean platform mooring cable.
The chemical component that the present invention designs makes full use of influence of the various alloying elements to phase transformation and microstructure, is formed few
Measure retained austenite, remaining is the complex phase microstructure based on tempered martensite and tempering bainite, while control P, S, N, O and
The content of H, guarantees intensity, low-temperature impact toughness and elongation percentage of steel etc., and production has ultra-high strength and toughness and strong plasticity matched
1100MPa grades of high strength steel materials of tensile strength can be used for ocean platform mooring cable, automobile and mechanical structure etc. and need height tough
The occasion of bar.
The present invention passes through rational designing chemical composition and combines optimization technique, develops 1100MPa grades of superelevation of tensile strength
Tough steel, this steel have excellent toughness, preferable elongation percentage and the contraction percentage of area at low temperature.Rolling or the bar forged exist
Tempering process is used after quenching, forms the matrix of tempered martensite and tempering bainite, retained austenite, is had on matrix thin
The Carbide Precipitation of change eliminates the internal stress of steel, has good structural homogenity.
Beneficial effects of the present invention:
The present invention improves C element content in terms of chemical component, and combines Ni, Mn constituent content of optimization, forms back
The complex phase microstructure of fiery bainite and tempered martensite, retained austenite, wherein Ni and Mn element is stabilization of austenite
Element, the Ni and Mn of addition content optimization will form retained austenite, while using Ni to the contribution for reducing stacking fault energy and Mn pairs
The contribution for improving tensile strength realizes microstructure of the present invention, while utilizing the Carbide Precipitation of Cr, Mo, Nb, V, Ti
Realize precipitation strength, therefore such microstructure has good low-temperature impact toughness and tensile property.
The present invention uses Quenching plus tempering process, obtains tempered martensite+tempering bainite and retained austenite group
It knits, yield strength >=900MPa, tensile strength >=1100MPa, yield tensile ratio 0.89~0.95, the Xia Shi Impact energy Ak v of the steel
(- 20 DEG C) >=70J, elongation percentage >=15%, the contraction percentage of area >=50%, such ultra-high strength and toughness steel have good intensity, low
Warm toughness and plasticity.
High-strength tenacity matching can be realized using primary quenching technique in steel grade of the present invention, and quenching process is omitted, and drops
Low production cost and carbon emission, belong to environmental-friendly steel.
The ingredient of steel of the present invention and technological design are reasonable, and process window is loose, can be in bar or plate producing line
Upper realization batch is commercially produced.
Detailed description of the invention
Fig. 1 is the microstructure morphology of 4 rod iron of the embodiment of the present invention.
Specific embodiment
Below with reference to embodiment and attached drawing, the present invention will be further described.These embodiments are only best to the present invention
The description of embodiment, does not have any restrictions to the scope of the present invention.
The ingredient of the embodiment of the present invention is shown in Table 1.The manufacturing method of the embodiment of the present invention includes: smelting, casting, heating, forging
It makes or rolls, be quenched and tempering.Molding or continuous casting can be used in casting process.During heating, heating temperature
Degree is 1050~1250 DEG C, finishing temperature or final forging temperature >=760 DEG C.During the rolling process, steel billet Direct Rolling can be used
To final specification, or using billet rolling to specified intermediate base size, then heated and be rolled down to final finished size.
Steel billet starts to roll after going out heating furnace, and air-cooled or slow cooling is entered after rolling.
Product of the present invention can be used for the occasion that ocean platform mooring cable etc. needs high-intensitive bar, the size of bar
Specification is up to diameter 180mm.
Specific embodiment is as follows:
Embodiment 1
By chemical component electric furnace or converter smelting shown in table 1, and it is cast into continuous casting billet or steel ingot, by continuous casting billet or steel ingot
1050 DEG C are heated to, finishing temperature is 800 DEG C, intermediate base size 220*220mm.Intermediate base is heated to 1070 DEG C, finishing temperature
760 DEG C, finished product bar specification isIt is air-cooled after rolling.Quenching temperature is 840 DEG C, and heating time is 30 minutes；
Tempering temperature is 500 DEG C, and tempering time is 30 minutes, air-cooled after tempering.
Embodiment 2
Embodiment is with embodiment 1, and wherein heating temperature is 1080 DEG C, and finishing temperature is 840 DEG C, intermediate base size 215*
215mm.Intermediate base is heated to 1100 DEG C, and 830 DEG C of finishing temperature, finished product bar specification isIt is air-cooled after rolling.Quenching
Heating temperature is 870 DEG C, and heating time is 100 minutes, and tempering temperature is 530 DEG C, and tempering time is 60 minutes, empty after tempering
It is cold.
Embodiment 3
Embodiment is with embodiment 1, and wherein heating temperature is 1120 DEG C, and finishing temperature is 920 DEG C, and finished product bar specification isIt is air-cooled after rolling.Quenching temperature is 900 DEG C, and heating time is 150 minutes, and tempering temperature is 550 DEG C, is returned
The fiery time is 100 minutes, air-cooled after tempering.
Embodiment 4
Embodiment is with embodiment 1, and wherein heating temperature is 1150 DEG C, and finishing temperature is 980 DEG C, and finished product bar specification isSlow cooling after rolling.Quenching temperature is 930 DEG C, and heating time is 150 minutes, and tempering temperature is 590 DEG C, is returned
The fiery time is 180 minutes, air-cooled after tempering.
Embodiment 5
Embodiment is with embodiment 1, and wherein heating temperature is 1200 DEG C, and finishing temperature is 1020 DEG C, finished product bar specification
ForSlow cooling after rolling.Quenching temperature is 980 DEG C, and heating time is 170 minutes, and tempering temperature is 610 DEG C,
Tempering time is 260 minutes, water cooling after tempering.
Embodiment 6
Embodiment is with embodiment 1, and wherein heating temperature is 1250 DEG C, and finishing temperature is 1020 DEG C, finished product bar specification
ForSlow cooling after rolling.Quenching temperature is 1040 DEG C, and heating time is 300 minutes, tempering temperature 650
DEG C, tempering time is 300 minutes, water cooling after tempering.
Mechanics Performance Testing is carried out to 1-6 steel of the embodiment of the present invention, test result is shown in Table 2.
From table 2 it can be seen that yield strength >=the 900MPa for the steel that the present invention produces, tensile strength >=1100MPa,
Xia Shi Impact energy Ak v (- 20 DEG C) >=70J, elongation percentage A >=15%, the contraction percentage of area >=50%.
Microstructure research is carried out to embodiment 4, optical microscope photograph is shown in Fig. 1.It will be seen from figure 1 that rod iron
Microstructure is retained austenite, tempered martensite and the tempering bainite tissue of refinement.
Claims (6)
1. a kind of tensile strength 1100MPa grades of ultra-high strength and toughness steel, chemical component weight percentage are as follows: C:0.245~
0.350%, Si:0.10~0.50%, Mn:0.20~1.20%, P≤0.015%, S≤0.003%, Cr:0.30~
1.20%, Mo:0.20~0.80%, Ni:2.00~3.70%, Cu:0~0.30%, Nb:0~0.08%, V:0~0.12%,
Al:0.01~0.08%, Ti:0.003~0.06%, Ca≤0.005%, H≤0.0002%, N≤0.0120%, O≤
0.0030%, remaining is Fe and inevitable impurity.
2. tensile strength 1100MPa grades of ultra-high strength and toughness steel according to claim 1, which is characterized in that the tensile strength
The microstructure of 1100MPa grades of ultra-high strength and toughness steel is tempered martensite+tempering bainite+residual austenite body tissue.
3. tensile strength 1100MPa grades of ultra-high strength and toughness steel according to claim 1 or 2, which is characterized in that the tension is strong
Spend yield strength >=900MPa, tensile strength >=1100MPa, -20 DEG C of Xia Shi Impact energy Ak v of 1100MPa grades of ultra-high strength and toughness steel
>=70J, elongation percentage >=15%, the contraction percentage of area >=50%.
4. the manufacturing method of tensile strength 1100MPa grades of ultra-high strength and toughness steel as described in any one of claims 1-3, including it is as follows
Step:
1) it smelts, cast
Chemical component according to claim 1 is smelted, is cast；
2) it heats
Heating temperature is 1050~1250 DEG C；
3) it rolls or forges
Finishing temperature >=760 DEG C or final forging temperature >=760 DEG C；
4) quenching heat treatment
Hardening heat is 840~1050 DEG C；
5) tempering heat treatment
Tempering temperature is 500~650 DEG C, air-cooled after tempering.
5. the manufacturing method of tensile strength 1100MPa grades of ultra-high strength and toughness steel according to claim 4, which is characterized in that institute
The microstructure for stating 1100MPa grades of ultra-high strength and toughness steel of tensile strength is tempered martensite+tempering bainite+retained austenite group
It knits.
6. the manufacturing method of tensile strength 1100MPa grades of ultra-high strength and toughness steel according to claim 4 or 5, which is characterized in that
Yield strength >=900MPa, tensile strength >=1100MPa, -20 DEG C of Xia Shi of the tensile strength 1100MPa grades of ultra-high strength and toughness steel
Impact energy Ak v >=70J, elongation percentage >=15%, the contraction percentage of area >=50%.
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Application publication date: 20190104 |