CN106119700B - A kind of 1180MPa grades of precipitation strength type high-strength high-plasticity steel and its manufacturing method - Google Patents
A kind of 1180MPa grades of precipitation strength type high-strength high-plasticity steel and its manufacturing method Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 149
- 239000010959 steel Substances 0.000 title claims abstract description 149
- 238000001556 precipitation Methods 0.000 title claims abstract description 43
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 15
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 49
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 36
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 27
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 24
- 239000000203 mixture Substances 0.000 claims abstract description 23
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 20
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 19
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 17
- 230000000717 retained effect Effects 0.000 claims abstract description 15
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 13
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 13
- 239000000126 substance Substances 0.000 claims abstract description 13
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 10
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 8
- 229910052760 oxygen Inorganic materials 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 238000009826 distribution Methods 0.000 claims abstract description 5
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 4
- 238000010438 heat treatment Methods 0.000 claims description 33
- 238000001816 cooling Methods 0.000 claims description 30
- 238000005096 rolling process Methods 0.000 claims description 27
- 238000000034 method Methods 0.000 claims description 26
- 238000005098 hot rolling Methods 0.000 claims description 9
- 238000005266 casting Methods 0.000 claims description 8
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 7
- 241001062472 Stokellia anisodon Species 0.000 claims description 3
- 239000010936 titanium Substances 0.000 description 44
- 239000010955 niobium Substances 0.000 description 27
- 229910052799 carbon Inorganic materials 0.000 description 26
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 23
- 238000013461 design Methods 0.000 description 18
- 230000008569 process Effects 0.000 description 17
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 16
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 16
- 239000011572 manganese Substances 0.000 description 16
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 14
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 14
- 239000013078 crystal Substances 0.000 description 12
- 230000000694 effects Effects 0.000 description 12
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 12
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 11
- 239000004411 aluminium Substances 0.000 description 10
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 9
- 239000005864 Sulphur Substances 0.000 description 9
- 235000013339 cereals Nutrition 0.000 description 9
- 239000010703 silicon Substances 0.000 description 7
- 238000010791 quenching Methods 0.000 description 6
- 230000000171 quenching effect Effects 0.000 description 6
- 230000003014 reinforcing effect Effects 0.000 description 6
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 5
- 230000015572 biosynthetic process Effects 0.000 description 5
- 150000001875 compounds Chemical class 0.000 description 5
- 239000011574 phosphorus Substances 0.000 description 5
- 238000001953 recrystallisation Methods 0.000 description 5
- 238000005496 tempering Methods 0.000 description 5
- 230000009466 transformation Effects 0.000 description 5
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 4
- 238000005516 engineering process Methods 0.000 description 4
- 239000001301 oxygen Substances 0.000 description 4
- 230000001376 precipitating effect Effects 0.000 description 4
- 238000009628 steelmaking Methods 0.000 description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 3
- 239000004615 ingredient Substances 0.000 description 3
- 150000004767 nitrides Chemical class 0.000 description 3
- 229910001562 pearlite Inorganic materials 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- 238000007670 refining Methods 0.000 description 3
- 238000003466 welding Methods 0.000 description 3
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 2
- 125000004429 atom Chemical group 0.000 description 2
- 229910001567 cementite Inorganic materials 0.000 description 2
- 238000009749 continuous casting Methods 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 2
- 125000004433 nitrogen atom Chemical group N* 0.000 description 2
- 230000008520 organization Effects 0.000 description 2
- 230000002265 prevention Effects 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 235000015170 shellfish Nutrition 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- INZDTEICWPZYJM-UHFFFAOYSA-N 1-(chloromethyl)-4-[4-(chloromethyl)phenyl]benzene Chemical compound C1=CC(CCl)=CC=C1C1=CC=C(CCl)C=C1 INZDTEICWPZYJM-UHFFFAOYSA-N 0.000 description 1
- 240000007594 Oryza sativa Species 0.000 description 1
- 235000007164 Oryza sativa Nutrition 0.000 description 1
- 238000003723 Smelting Methods 0.000 description 1
- GUWKQWHKSFBVAC-UHFFFAOYSA-N [C].[Au] Chemical compound [C].[Au] GUWKQWHKSFBVAC-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000004364 calculation method Methods 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 235000019362 perlite Nutrition 0.000 description 1
- 239000010451 perlite Substances 0.000 description 1
- 229920001296 polysiloxane Polymers 0.000 description 1
- 238000011946 reduction process Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 230000033764 rhythmic process Effects 0.000 description 1
- 235000009566 rice Nutrition 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 125000004434 sulfur atom Chemical group 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- 238000001291 vacuum drying Methods 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
Classifications
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing 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
- C21D2211/002—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
- C21D2211/005—Ferrite
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
A kind of 1180MPa grades of precipitation strength type high-strength high-plasticity steel and its manufacturing method, the steel chemical composition weight percent are：C：0.15~0.20%, Si：0.8~2.0%, Mn：1.5~2.0%, P≤0.015%, S≤0.005%, O≤0.003%, Al：0.4~1.0%, N≤0.005%, Nb：0.03~0.06%, Ti：0.1~0.2%, V≤0.40%, remaining is Fe and inevitable impurity, and need to meet following relation simultaneously：0.10%≤Nb+Ti≤0.25%；0.02%≤(Ti 3.42N 3S)/4+V/4.24+Nb/7.74≤0.15%；2.5≤Al/C≤5.0.The microstructure of steel of the present invention be ferrite, bainite and retained austenite, the transgranular distribution Nano-Scaled Carbide of ferrite, ferrite average grain size≤5 μm, Nano-Scaled Carbide size≤10nm；Width≤5 μm of lath of bainite, yield strength >=1000MPa, tensile strength >=1180MPa, elongation percentage >=15% show excellent high intensity and high-ductility matching.
Description
Technical field
The invention belongs to hot-rolling high-strength steel fields, and in particular to a kind of 1180MPa grades of precipitation strength type high-strength high-plasticity
Steel and its manufacturing method.
Background technology
In automobile especially passenger car field, high-strength thinned or vehicle structure lightweight has become automobile factory in the world
The important research direction of business.Different from the high-strength thinned and lightweight trend of passenger car, the lightweight work progress of commercial car is very
Slowly.Main cause one is since the universal surcharge ratio of commercial car is more serious, and the designer of commercial car is to the design margin of structure
It is very big；Meanwhile commercial car itself and loading capacity are larger, rigidity is difficult to ensure that sometimes after being thinned using high-strength steel；It is another
Aspect is the reason is that since commercial car for passenger car with respect to Price Sensitive customers are belonged to, and it is generally desirable to the intensity in steel plate by user
While raising, price had better not improve too much.Therefore, no matter from the demand willingness used high-strength steel or its own
Working ability and price are born etc. all so that the high-strength of commercial car is thinned and weight reduction process is made slow progress.But at some
Position still needs using high-strength or even super-high strength steel, such as collision prevention girders.With continuous stringent, the commercial car of energy-saving and emission-reduction requirement
Processing and user should see clearly industry development trend, the lightweight of commercial car also will be a kind of following trend.Therefore, open
The excellent high-strength steel of volatility also will be following development trend.
At present, tensile strength mainly adds micro- conjunction in composition design in the high-strength steel of more than 1180MPa ranks using higher carbon
Gold element, the method for generally use out-line quenching add-back fire in technique.Under normal circumstances, after quenching+tempering steel plate property
It can show as yield strength and tensile strength ratio is higher, even close to 1.0 usually more than 0.90, and elongation percentage is usually 10
± 1%.To ensure user's cold forming processing request, user is usually required that on the basis of more than tensile strength 1180MPa is kept,
Elongation percentage is improved to more than 15%.This is almost for traditional organization design thinking and quenching plus lonneal technique
Impossible index.This is because both at home and abroad countless theories and result of the test also it was demonstrated that using traditional quenching+
Tempering process manufactures 1180MPa grades of super-high strength steel, and elongation percentage and hole expansibility index can not meet user's requirement.
Only Japan JFE etc. develops 1180MPa grades of high-strength steel Japan Patent JP5386961B2 using nanometer technology and adopts at present
1180MPa grades of high-strength steel are manufactured with microalloying ingredient design and sub-sectional cooling and average tempering technique, tensile strength reaches
To 1180MPa, elongation percentage is up to more than 15%, and using high Nb in composition design, cost is higher, and has a step in manufacturing process
Average tempering technique.
The content of the invention
It is an object of the invention to provide a kind of 1180MPa grades of precipitation strength type high-strength high-plasticity steel and its manufacturers
Method, yield strength >=1000MPa of the high-strength high-plasticity steel, tensile strength >=1180MPa, elongation percentage >=15% are shown
Excellent intensity and plasticity matching, can be applicable to wheel etc. needs favorable forming property and high-strength thinned position.
In order to achieve the above objectives, the technical scheme is that：
The Si main purposes of present invention addition high level：First is the work of ferrite formation during expansion sub-sectional cooling
Skill window, second is to inhibit being formed and finally obtaining more retained austenite for carbide (mainly cementite)；Addition compared with
High Al main purposes are under conditions of carbon and manganese content are relatively high, accelerate ferrite Cambium periodicity process；Addition compared with
High Ti main purposes be after rolling the air-cooled stage the tiny Nano-Scaled Carbide of disperse is formed in ferrite with strengthen iron element
Body；In addition, compound addition Nb and Ti can also ensure to obtain tiny austenite in rolling sequence, so as to the air-cooled stage after rolling
Obtain more tiny ferrite；Add in higher V main purposes：First is further improved by force by the precipitation strength of VC
Degree, second is to have good effect to the follow-up welding point softening for improving super-high strength steel.Based on mentioned component and technological design
Thinking can obtain the 1180MPa grade hot rolling super-high strength steels with superhigh intensity and plasticity matched well.
A kind of 1180MPa grades of precipitation strength type high-strength high-plasticity steel, chemical component weight percentage are：C：0.15~
0.20%, Si：0.8~2.0%, Mn：1.5~2.0%, P≤0.015%, S≤0.005%, O≤0.003%, Al：0.4~
1.0%, N≤0.005%, Ti：0.1~0.2%, Nb：0.03~0.06%, V≤0.40%, remaining is for Fe and inevitably
Impurity, and above-mentioned element need to meet following relation simultaneously：0.10%≤Nb+Ti≤0.25%, 0.02%≤(Ti-3.42N-
3S)/4+V/4.24+Nb/7.74≤0.15%, 2.5≤Al/C≤5.0.
Preferably, in the chemical composition of the high-strength high-plasticity steel：C：0.16~0.18%, by weight percentage.
Preferably, in the chemical composition of the high-strength high-plasticity steel：Si：1.2~1.8%, by weight percentage.
Preferably, in the chemical composition of the high-strength high-plasticity steel：Mn：1.6~1.8%, by weight percentage.
Preferably, in the chemical composition of the high-strength high-plasticity steel：Al：0.5~0.8%, by weight percentage.
Further, the microstructure of the high-strength high-plasticity steel be ferrite, bainite and retained austenite, ferrite
Transgranular distribution Nano-Scaled Carbide, ferrite average grain size≤5 μm, Nano-Scaled Carbide size≤10nm；Bainite plate
Width≤5 μm of item.
Preferably, in the microstructure of the high-strength high-plasticity steel lath of bainite width≤3 μm.
Preferably, volume fraction shared by ferrite is 20~35% in the microstructure of the high-strength high-plasticity steel, shellfish
Volume fraction shared by family name's body is 60~70%, and volume fraction shared by retained austenite is 5~10%.
Yield strength >=1000MPa of high-strength high-plasticity steel of the present invention, tensile strength >=1180MPa, elongation percentage
>=15%.
In the composition design of steel of the present invention：
Carbon：Carbon is one of the basic element in steel and important element in the present invention.Carbon is former as the gap in steel
Son plays very important effect to the intensity for improving steel, and the yield strength and tensile strength on steel influence maximum.In the present invention
In, in order to obtain the super-high strength steel that tensile strength reaches 1180MPa grades, except ferrite average grain size must is fulfilled for≤5 μm
Outside, it is necessary to by the further reinforced ferrite intensity of nanometer precipitated phase (size≤10nm)；In addition it is necessary to by tiny
Bainite strengthens and the TRIP effects of retained austenite.Carbon content is at least more than 0.15% in steel；Carbon content is not yet simultaneously
Can be too high, it is unfavorable to the welding performance of steel if carbon content is more than 0.20%.Therefore, carbon content must be controlled below 0.20%,
And meet 0.02%≤(Ti-3.42N-3S)/4+V/4.24+Nb/7.74≤0.15% between Nb, Ti and V content.To sum up,
Carbon content should be controlled 0.15~0.20% in the present invention, and preferred scope is 0.16~0.18%.
Silicon：Silicon is also the basic element in steel, while is also one of important element in the present invention.This is because it to obtain
Tensile strength reaches the high-strength high-plasticity steel of more than 1180MPa, ferritic size and number are on the one hand controlled, using receiving
Rice, which is precipitated, improves ferritic intensity；Also to improve the intensity of bainite by refining lath of bainite simultaneously.This need into
Set up the content that carbon and manganese are properly increased in meter separately, and carbon and manganese are all to expand austenitic area, the element of stable austenite.In hot rolling
(usually≤10s) is difficult to form sufficient amount of ferrite in very short time in process air cooler, this just needs addition is higher to contain
The element silicon of amount.The addition of silicon can be obviously promoted ferrite and be formed, and expand the process window that ferrite is formed, and purify ferrite,
Partial reinforment can also be played the role of simultaneously.Another important function of silicon in steel is to inhibit the shape of cementite in phase transition process
Into, be conducive to improve final residual austenite content.These effects of silicon must when its content reaches more than 0.8% ability table
Reveal and；But the content of silicon also should not be too high, otherwise steel plate degraded toughness.Therefore, in steel silicone content be normally controlled in 0.8~
Between 2.0%, preferred scope is between 1.2~1.8%.
Manganese：Manganese is element most basic in steel, while is also one of most important element in the present invention.It is well known that manganese
It is the important element for expanding austenite phase field, the critical quenching rate of steel, stable austenite can be reduced, crystal grain thinning is postponed
Austenite from being transformed into perlite.In the present invention, to ensure the high intensity of steel plate, manganese content should be controlled more than 1.5%, manganese
Content is relatively low, and overcooling austenite is not sufficiently stable, and cools down the tissue for being easily changed into pearlite type in process air cooler；Meanwhile manganese
Content is generally also no more than 2.0%, if more than 2.0%, manganese segregation easily occurs for when steel-making, while easily occurs during sheet billet continuous casting
Hot tearing.Therefore, manganese content control is 1.5~2.0% in steel of the present invention, and preferred scope is 1.6~1.8%.
Phosphorus：Phosphorus is the impurity element in steel.Phosphorus easily segregation is on crystal boundary, in steel during the content of phosphorus higher (>=0.1%),
Form Fe2P is precipitated around crystal grain, reduces the plasticity and toughness of steel, therefore phosphorus content is more low better, and general control is 0.015%
Within preferably and do not improve steel-making cost.
Sulphur：Sulphur is the impurity element in steel.Sulphur in steel usually combines to form MnS with manganese and is mingled with, especially when sulphur and manganese
Content it is higher when, more MnS will be formed in steel, and MnS has certain plasticity in itself, in the follow-up operation of rolling
MnS rolls the transverse tensile property for deforming, reducing steel plate in edge.In high Ti steel, sulphur can also form Ti with Ti and C4C2S2
Compound consumes part Ti so that the quantity of effective Ti is reduced, and influences final precipitating reinforcing effect.Therefore, sulphur contains in steel
Amount is more low better, and when actual production is normally controlled within 0.005%.
Aluminium：Aluminium is one of important element in the present invention.Due to high-strength high-plasticity steel involved in the present invention, tension is strong
Degree reaches more than 1180MPa, and the content of carbon and manganese is relatively high in steel, and overcooling austenite is relatively stable, is difficult in process air cooler
Sufficient amount of ferrite is formed, therefore, it is necessary to add in more aluminium in composition design ferrite is promoted to be formed.Aluminium adds
Dosage is mainly related with carbon content, and carbon content is higher, and the addition of aluminium is also higher.In the present invention in the composition range of carbon, carbon
The relation of 2.5≤Al/C≤5.0 should be met between aluminium.Aluminium content is too low, it is difficult to form enough ferrites；Aluminium content is excessively high,
Continuous casting billet Longitudinal Surface Cracks are more serious.Therefore, between 0.4~1.0%, preferred scope is for aluminium content control in steel of the present invention
0.5~0.8%.
Nitrogen：Nitrogen belongs to impurity element in the present invention, and content is more low better.Nitrogen is also inevitable element in steel,
Under normal conditions, if without Special controlling in steelmaking process, the residual content of nitrogen in steel is usually≤0.005%.These are solid
Molten or free nitrogen must be fixed by forming certain nitride, and otherwise free nitrogen-atoms is to the impact flexibility of steel
It is very unfavorable, and the sawtooth for being readily formed during belt steel rolling overall length splits defect.Pass through addition in the present invention
Strong carbide or nitride forming element Ti form stable TiN so as to fixed nitrogen-atoms.Therefore, the content control of nitrogen exists
It is within 0.005% and more low better.
Niobium：Niobium is one of most important element in the present invention.Niobium is with the compound addition of titanium to heating and operation of rolling austenite
Grain refining effect is most notable, and the effect of fining austenite grains is much larger than single niobium, titanium and vanadium after niobium and the compound addition of titanium
The effect of addition.After niobium is added in steel, at high temperature such as the heating steel billet stage, strong solute between the niobium and crystal boundary of solid solution
Effect of dragging can refine austenite grain during heating steel billet；In rolling sequence, since niobium has the work for improving recrystallization temperature
With compared to titanium, vanadium, aluminum element, the effect that niobium improves recrystallization temperature is most strong, by being rolled on recrystallization temperature
System, can obtain the austenite of tiny hardening, and equivalent grain size is small, and dislocation density is high, can be with during ferritic transformation
Obtain very tiny ferrite crystal grain；Meanwhile (Nb, Ti) (C, the N) of the 20-40nm in rolling sequence formation can be more into one
Walk fining austenite grains.Fine austenite crystal grain during high-temperature heating and the more tiny Ovshinsky containing high dislocation density during rolling
Body crystal grain ensures the ferritic abundant refinement of phase-change product and reinforcing during cooling phase-change.The content of niobium is at least up to
More than 0.03% just has the effect for significantly improving recrystallization temperature；The addition of niobium is also unsuitable excessive, is normally controlled in
Less than 0.06%.The addition of niobium and titanium should also meet 0.10%≤Nb+Ti≤0.25%.
Titanium：Titanium is one of important element in the present invention.C, N, S atom have very strong combination power in titanium and steel.The present invention
Composition design thinking be primarily intended to obtain small and dispersed Nano-Scaled Carbide rather than nitride.The combination power of titanium and nitrogen is big
Combination power between titanium and carbon, in order to reduce the forming amount of TiN in steel to the greatest extent, the content of nitrogen in steel should control more low more
It is good.Add in high level titanium main purpose be in order in austenite during ferritic transformation, in ferrite or bayesian
More Nano-Scaled Carbides are formed in body；Similarly, adding in higher vanadium main purpose is formed more in bainite
Nano vanadium carbide particle further improves the effect of dispersion-strengtherning.
Key element carbon, titanium, sulphur and vanadium should meet certain relation i.e. 0.02%≤(Ti-3.42N-3S)/4 in the present invention
+ V/4.24+Nb/7.74≤0.15% could obtain ferrite and bainite precipitation strength super-high strength steel.It is demonstrate,proved by a large number of experiments
Real, carbon must meet above-mentioned relation with titanium, sulphur, the content of vanadium, and the Nano-Scaled Carbide otherwise formed in steel cannot utmostly be sent out
It waves in disperse educt reinforcing effect or steel and is likely to occur a small amount of pearlitic structrure so that the intensity of steel plate is difficult to reach
The high intensity of 1180MPa.The optimal Precipitation Temperature of Nano-Scaled Carbide is mainly closely related with the content of titanium, sulphur and vanadium.Through
Crossing theoretical calculation and experiment confirms that within the temperature range of 650~750 DEG C, titanium can play the content of optimal precipitating reinforcing effect
Scope is between 0.10~0.20%.
Vanadium：Vanadium is one of key element in the present invention.Vanadium is similar with titanium, due to its carbonitride consolidating in austenite
Solubility is larger, and is usually precipitated in ferrite.Only had using low-carbon titaniferous, vanadium steel its attainable maximum pulling strength of institute
800~900MPa or so, to continue the intensity of raising ferrite-bainite type high-strength steel, it is necessary to improve carbon content, but carbon contains
Amount increases bringing the result is that there is banding pearlite in tissue when high temperature section is air-cooled；Vanadium is also carbide, is added
Extra carbon can be fixed by entering suitable vanadium, can not only further function as precipitating reinforcing effect, but also it is air-cooled to also avoid high temperature
When pearlite formation.In addition, 1180MPa grades of high-strength steel according to the present invention in follow-up welding process it can also happen that connector
Ruckbildung, this can preferably be solved the problems, such as by adding in suitable vanadium.According to theory analysis and experimental study, the content of vanadium
It should control in the range of≤0.4%, and certain relation i.e. 0.02%≤(Ti- should be met between Nb, Ti, N, S and C
3.42N-3S)/4+V/4.24+Nb/7.74≤0.15%.
Oxygen：Oxygen is inevitable element in steelmaking process, for the purpose of the present invention, in steel the content of oxygen by aluminium deoxidation it
Less than 0.003% can generally be reached afterwards, significant adverse will not be caused to influence the performance of steel plate.Therefore, by the oxygen in steel
Content is controlled within 0.003%.
The manufacturing method of 1180MPa grades of precipitation strength type high-strength high-plasticity steel of the present invention, includes the following steps：
1) smelt, cast
It smelted, refined by above-mentioned chemical composition, being cast as strand or ingot casting；
2) strand or ingot casting heating
Heating temperature >=1230 DEG C, when heating time 1~2 is small；
3) hot rolling+sub-sectional cooling+is batched
Start rolling temperature is 1080~1200 DEG C, carried out at 1000 DEG C or more 3~5 passage roughing and accumulative deflection >=
50%；Intermediate base treats temperature as 900~950 DEG C, carries out 3~5 passage finish rolling and accumulative deflection >=80%；Finishing temperature
For 800~900 DEG C, after finish to gauge with the cooling rate of >=100 DEG C/s by steel plate water cooling to 650~750 DEG C；After air-cooled 5~10 seconds,
It is batched to 350~500 DEG C with the cooling rate water cooling of >=100 DEG C/s, is cooled to room temperature after batching with the cooling rate of≤20 DEG C/h again.
The reasons why design and manufacture technology of the present invention, is as follows：
For the high-strength steel of high Ti precipitation strengths type, heating temperature is a critically important technological parameter.With it is general
Logical high-strength steel is compared, and it is the slab in heating that high Ti steel of the invention, which designs higher heating temperature (>=1230 DEG C) main purpose,
Middle solid solution Ti atoms as much as possible.Since the carbonitride solid solubility temperature of Ti is usually very high (>=1300 DEG C), is making steel or connecting
The different phase of casting and the operation of rolling can be precipitated, this allows for finally can be used to the Ti contents for playing the role of precipitation strength just
It is very low.It is therefore necessary to ensure high heating temperature is possible to obtain more nano-scale carbons in air-cooled phase process after rolling
Compound, therefore, the present invention claims steel plate minimum heating temperature it is necessary >=1230 DEG C；The upper limit of heating temperature is heated according to scene
Stove is actually accessible or the temperature that can bear is limited, and heating temperature does not set upper limit requirement in principle.In order to save energy consumption, lead to
Often actual maximum heating temperature is controlled at≤1300 DEG C.
For high Ti steel, the heating time of slab for heating temperature, influences much smaller.Theoretically
For, as long as heating temperature reaches the balance solution temperature of the carbonitride of Ti, solution rate is very fast.Therefore in this stage,
Heating time is mainly to ensure that slab can be grilled thoroughly uniformly as main target.Certainly, heating time can not be too long, otherwise
The carbonitride of the undissolved Ti of high temperature is very likely roughened and grows up, the carbonitride of these coarse Ti is in austenite
Grain boundaries are precipitated, and reduce the bond strength of crystal boundary, and easily disconnected base phenomenon occurs in heating furnace for slab in heating process.Cause
This, it is different according to slab thickness, heating temperature be normally controlled in 1~2 it is small when.
In rolling mill practice design, in order to coordinate the composition design of high Ti, the heating temperature of steel billet must it is sufficiently high (as >=
1230 DEG C) with ensure there are Ti atoms as much as possible to be solid-solubilized in slab；In roughing and finish rolling stage, the rhythm of the operation of rolling should
It is rapidly completed as far as possible, avoids the Carbonitride Precipitation in roughing and finish rolling stage excessive Ti.It should be with high cooling rate after finish to gauge
For (>=100 DEG C/s) quick water cooling to two-phase section and air-cooled 5~10 seconds in two-phase section, main purpose is ferritic in air-cooled formation
A large amount of tiny TiC are precipitated in the process.If this is because rolling after cooling velocity it is slower, the Ovshinsky of steel plate internal distortions
Body can be completed in a relatively short time partial, re-crystallization process, and austenite grain is grown up at this time.Relatively coarse austenite
When ferrite transformation occurs for subsequent cooling procedure, the ferrite crystal grain of formation is more coarse, usually between 10~20 μm,
It is unfavorable to the intensity of raising steel plate.Rolling mill practice schematic diagram of the present invention is referring to Fig. 1.Steel plate organization design thinking of the present invention is nanometer
Precipitation strength ferrite, bainite and retained austenite tissue.
The high intensity of steel plate is from two aspects：When nanometer precipitation strength ferrite, second is that tiny bainite.According to warp
The Orowan mechanism of allusion quotation, nano-carbide is to the contribution of intensity about between 200~400MPa.But only nanometer precipitation strength
Far from enough, the high intensity of steel plate must also come from tiny bainite.Reach the intensity rank of 1180MPa, ferrite
The size of crystal grain must be controlled below 5 μm, the width of lath of bainite must below 0.5 μm, preferably below 0.3 μm,
This just needs steel plate that must be quickly cooled to two-phase section after finish to gauge, is quickly cooled to again afterwards by 5~10s is air-cooled
350~500 DEG C carry out bainite transformation and precipitation.Therefore, the cooling velocity after strip finish to gauge should sufficiently fast (>=100 DEG C/s),
It avoids forming ferrite in continuous cooling process, and should be that the tiny ferrite in part is formed in strip process air cooler and is received
Meter level carbide, the austenite that remaining part does not change are further continued for being cooled to 350~500 DEG C soon with the cooling rate of >=100 DEG C/s, with
The nanometer for carrying out bainitic transformation or VC is precipitated, and slow cooling to room temperature obtains 5~10% retained austenite, and specific cooling technique is shown
It is intended to as shown in Figure 2.
The present invention coordinates innovative hot rolling technology that can obtain intensity and plasticity by ingenious rational composition design
Excellent 1180MPa grade nanometer precipitation strength super-high strength steels.Steel plate is organized as a nanometer precipitation strength ferrite, bainite and residual
Remaining austenite, ferrite average grain size are≤5 μm, and ferrite form is the spindle-type such as near, and the transgranular a large amount of disperses of distribution are thin
Small Nano-Scaled Carbide (size≤10nm).While tensile strength reaches 1180MPa high intensity, steel plate has >=15%
High-elongation.
In composition design, the addition main purpose one of high Ti contents is to coordinate Austria of refinement heating and rolling sequence with Nb
Family name's body crystal grain, followed by order to, mainly in the tiny Nano-Scaled Carbide of ferrite diffusion-precipitation, be risen during strip coiling
To strong precipitating reinforcing effect；It is then to further increase the quantity of nanometer precipitated phase to add in a certain amount of V, is played stronger
Dispersion-strengthened effect；And the design of carbon content should proof strength, while to be also engaged with the content of Nb, Ti and V, it is necessary to
Meet following relation：0.02%≤(Ti-3.42N-3S)/4+V/4.24+Nb/7.74≤0.15%, while required by cooperation
Rolling mill practice, the microstructure of final ferrite, bainite and the retained austenite composition for obtaining nanometer precipitation strength, obtains height
The advanced high-strength steel of intensity high-ductility.
Beneficial effects of the present invention：
(1) present invention uses the composition design thinking of relatively economical, while coordinates existing hot continuous rolling producing line that can give birth to
Output has the advanced high-strength steel of nanometer precipitation strength type of superhigh intensity and high-elongation.
(2) present invention produces yield strength >=1000MPa, tensile strength >=1180MPa, elongation percentage >=15%, and thickness
The hot rolling precipitation strength type high-strength high-plasticity steel plate of degree≤6mm, the steel plate show excellent high intensity and plasticity matching, can
High-strength thinned place is needed applied to automobile chassis, crossbeam, center pillar, side bar etc., is had broad application prospects.
Description of the drawings
Fig. 1 is present invention heating and rolling mill practice schematic diagram.
Fig. 2 is roller repairing process schematic representation of the present invention.
Fig. 3 is that TEM photos are precipitated in the transgranular typical nanometer of ferrite in 3 steel plate of the embodiment of the present invention.
Specific embodiment
With reference to embodiment and attached drawing, the present invention will be further described.
Table 1 is the ingredient of steel of the embodiment of the present invention, and table 2 is the fabrication process parameters of steel of the embodiment of the present invention, and table 3 is this hair
The performance of bright embodiment steel.
Technological process of the embodiment of the present invention is：Converter or electric furnace smelting → vacuum drying oven double refining → strand or ingot casting → steel
Rear sub-sectional cooling → coil of strip is rolled in base (ingot) heating → hot rolling+, and wherein key process parameter is referring to table 2.
Fig. 3 is that TEM photos are precipitated in the transgranular typical nanometer of ferrite in 3 steel plate of the embodiment of the present invention.It can from Fig. 3
Go out, the Nano-Scaled Carbide size of the transgranular precipitation of iron element is about 6 ± 1nm.Just because of the nanometer being precipitated inside ferrite crystal grain
Level carbide substantially increases the intensity of steel plate, and the plasticity of steel plate is together improved with the retained austenite in steel.
As known from Table 3, the yield strength of the high-strength steel obtained using ingredient provided by the present invention and processing route >=
1000MPa, tensile strength >=1180MPa, elongation percentage >=15%, hence it is evident that better than the extension of traditional quenching+tempering type high-strength steel
Rate.The good intensity of steel plate of the present invention and plasticity matching come from fine ferrite, the shellfish of high intensity of its nanometer of precipitation strength
The retained austenite of family name's body and high level (percentage by volume is 5~10%), the composition being had excellent performance just because of these
The cooperation of phase so that there is steel plate excellent intensity and plasticity to match, and can apply and automobile chassis, structural member, wheel, collision prevention girders
Wait components.
Claims (17)
1. a kind of 1180MPa grades of precipitation strength type high-strength high-plasticity steel, chemical component weight percentage are：C：0.15~
0.20%, Si：0.8~2.0%, Mn：1.6~1.8%, P≤0.015%, S≤0.005%, O≤0.003%, Al：0.4~
1.0%, N≤0.005%, Ti：0.1~0.2%, Nb：0.03~0.06%, V≤0.40%, remaining is for Fe and inevitably
Impurity, and above-mentioned element need to meet following relation simultaneously：
0.10%≤Nb+Ti≤0.25%；
0.02%≤(Ti-3.42N-3S)/4+V/4.24+Nb/7.74≤0.15%；
2.5≤Al/C≤5.0；
The manufacturing method of the 1180MPa grades of precipitation strength type high-strength high-plasticity steel includes the following steps：
1) smelt, cast
It smelted, refined by above-mentioned chemical composition, being cast as strand or ingot casting；
2) strand or ingot casting heating
Heating temperature >=1230 DEG C, when heating time 1~2 is small；
3) hot rolling+sub-sectional cooling+is batched
Start rolling temperature is 1080~1200 DEG C, and 3~5 passage roughing and accumulative deflection >=50% are carried out at 1000 DEG C or more；
Intermediate base treats temperature as 900~950 DEG C, then carries out 3~5 passage finish rolling and accumulative deflection >=80%；Finishing temperature is
800~900 DEG C, after finish to gauge with the cooling rate of >=100 DEG C/s by steel plate water cooling to 650~750 DEG C；After air-cooled 5~10 seconds, then
It is batched to 350~500 DEG C with the cooling rate water cooling of >=100 DEG C/s, is cooled to room temperature after batching with the cooling rate of≤20 DEG C/h.
2. 1180MPa grades of precipitation strength type high-strength high-plasticity steel according to claim 1, which is characterized in that the height
In the chemical composition of intensity high-ductility steel：C：0.16~0.18%, by weight percentage.
3. 1180MPa grades of precipitation strength type high-strength high-plasticity steel according to claim 1, which is characterized in that the height
In the chemical composition of intensity high-ductility steel：Si：1.2~1.8%, by weight percentage.
4. 1180MPa grades of precipitation strength type high-strength high-plasticity steel according to claim 1, which is characterized in that the height
In the chemical composition of intensity high-ductility steel：Al：0.5~0.8%, by weight percentage.
5. according to 1180MPa grades of precipitation strength type high-strength high-plasticity steel of claim 1-4 any one of them, feature exists
In the microstructure of, the high-strength high-plasticity steel be ferrite, bainite and retained austenite, the transgranular distribution nanometer of ferrite
Level carbide, ferrite average grain size≤5 μm, Nano-Scaled Carbide size≤10nm, the μ of the width of lath of bainite≤5
m。
6. 1180MPa grades of precipitation strength type high-strength high-plasticity steel according to claim 5, which is characterized in that the height
Width≤3 μm of lath of bainite in the microstructure of intensity high-ductility steel.
7. 1180MPa grades of precipitation strength type high-strength high-plasticity steel according to claim 5, which is characterized in that the height
Volume fraction shared by ferrite is 20~35% in the microstructure of intensity high-ductility steel, volume fraction shared by bainite for 60~
70%, volume fraction shared by retained austenite is 5~10%.
8. 1180MPa grades of precipitation strength type high-strength high-plasticity steel according to claim 6, which is characterized in that the height
Volume fraction shared by ferrite is 20~35% in the microstructure of intensity high-ductility steel, volume fraction shared by bainite for 60~
70%, volume fraction shared by retained austenite is 5~10%.
9. according to 1180MPa grades of precipitation strength type high-strength high-plasticity steel of claim 1-4 any one of them, feature exists
In, yield strength >=1000MPa of the high-strength high-plasticity steel, tensile strength >=1180MPa, elongation percentage >=15%.
10. 1180MPa grades of precipitation strength type high-strength high-plasticity steel according to claim 5, which is characterized in that the height
Yield strength >=1000MPa of intensity high-ductility steel, tensile strength >=1180MPa, elongation percentage >=15%.
11. according to 1180MPa grades of precipitation strength type high-strength high-plasticity steel of claim 6-8 any one of them, feature exists
In, yield strength >=1000MPa of the high-strength high-plasticity steel, tensile strength >=1180MPa, elongation percentage >=15%.
12. the manufacturing method of 1180MPa grades of precipitation strength type high-strength high-plasticity steel as described in claim any one of 1-11,
Include the following steps：
1) smelt, cast
It smelted by any one of the claim 1-4 chemical compositions, refined, be cast as strand or ingot casting；
2) strand or ingot casting heating
Heating temperature >=1230 DEG C, when heating time 1~2 is small；
3) hot rolling+sub-sectional cooling+is batched
Start rolling temperature is 1080~1200 DEG C, and 3~5 passage roughing and accumulative deflection >=50% are carried out at 1000 DEG C or more；
Intermediate base treats temperature as 900~950 DEG C, then carries out 3~5 passage finish rolling and accumulative deflection >=80%；Finishing temperature is
800~900 DEG C, after finish to gauge with the cooling rate of >=100 DEG C/s by steel plate water cooling to 650~750 DEG C；After air-cooled 5~10 seconds, then
It is batched to 350~500 DEG C with the cooling rate water cooling of >=100 DEG C/s, is cooled to room temperature after batching with the cooling rate of≤20 DEG C/h.
13. the manufacturing method of 1180MPa grades of precipitation strength type high-strength high-plasticity steel according to claim 12, feature
It is, the microstructure of the high-strength high-plasticity steel is ferrite, bainite and retained austenite, and the transgranular distribution of ferrite is received
Meter level carbide, ferrite average grain size≤5 μm, Nano-Scaled Carbide size≤10nm, width≤5 of lath of bainite
μm。
14. the manufacturing method of 1180MPa grades of precipitation strength type high-strength high-plasticity steel according to claim 13, feature
It is, width≤3 μm of lath of bainite in the microstructure of the high-strength high-plasticity steel.
15. the manufacturing method of the 1180MPa grade precipitation strength type high-strength high-plasticity steel according to claim 13 or 14,
It is characterized in that, volume fraction shared by ferrite is 20~35% in the microstructure of the high-strength high-plasticity steel, bainite institute
It is 60~70% to account for volume fraction, and volume fraction shared by retained austenite is 5~10%.
16. according to the manufacturer of 1180MPa grades of precipitation strength type high-strength high-plasticity steel of claim 12-14 any one of them
Method, which is characterized in that yield strength >=1000MPa of the high-strength high-plasticity steel, tensile strength >=1180MPa, elongation percentage
>=15%.
17. the manufacturing method of 1180MPa grades of precipitation strength type high-strength high-plasticity steel according to claim 15, feature
It is, yield strength >=1000MPa of the high-strength high-plasticity steel, tensile strength >=1180MPa, elongation percentage >=15%.
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| CN118064797A (en) * | 2022-11-23 | 2024-05-24 | 宝山钢铁股份有限公司 | Nano precipitation strengthening ultra-high strength steel and manufacturing method thereof |
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| CN105154769A (en) * | 2015-09-18 | 2015-12-16 | 宝山钢铁股份有限公司 | 780 MPa hot-rolled high-strength steel with high hole expansion ratio and manufacturing method thereof |
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| CN105154769A (en) * | 2015-09-18 | 2015-12-16 | 宝山钢铁股份有限公司 | 780 MPa hot-rolled high-strength steel with high hole expansion ratio and manufacturing method thereof |
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