CN109136779A - A kind of martensitic matrix 1100MPa grades of rare earths Q&P steel Preparation Method - Google Patents
A kind of martensitic matrix 1100MPa grades of rare earths Q&P steel Preparation Method Download PDFInfo
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- CN109136779A CN109136779A CN201810924896.0A CN201810924896A CN109136779A CN 109136779 A CN109136779 A CN 109136779A CN 201810924896 A CN201810924896 A CN 201810924896A CN 109136779 A CN109136779 A CN 109136779A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 89
- 239000010959 steel Substances 0.000 title claims abstract description 89
- 229910000734 martensite Inorganic materials 0.000 title claims abstract description 25
- 238000002360 preparation method Methods 0.000 title claims abstract description 18
- 239000011159 matrix material Substances 0.000 title claims abstract description 17
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 22
- 238000005192 partition Methods 0.000 claims abstract description 19
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 19
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 18
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 17
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 15
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 14
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 14
- 238000010438 heat treatment Methods 0.000 claims abstract description 12
- 239000012535 impurity Substances 0.000 claims abstract description 11
- 238000004321 preservation Methods 0.000 claims abstract description 11
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 11
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 11
- 229910052796 boron Inorganic materials 0.000 claims abstract description 10
- 229910052727 yttrium Inorganic materials 0.000 claims abstract description 10
- 238000003723 Smelting Methods 0.000 claims abstract description 9
- 238000005098 hot rolling Methods 0.000 claims abstract description 9
- 238000005275 alloying Methods 0.000 claims abstract description 8
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 8
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 8
- 238000005554 pickling Methods 0.000 claims abstract description 8
- 238000005097 cold rolling Methods 0.000 claims abstract description 7
- 239000004615 ingredient Substances 0.000 claims abstract description 7
- 238000002844 melting Methods 0.000 claims abstract description 6
- 239000000843 powder Substances 0.000 claims abstract description 6
- 238000007670 refining Methods 0.000 claims abstract description 5
- 238000001291 vacuum drying Methods 0.000 claims abstract description 5
- 238000000034 method Methods 0.000 claims description 42
- 230000008569 process Effects 0.000 claims description 38
- 239000000463 material Substances 0.000 claims description 26
- 239000011572 manganese Substances 0.000 claims description 22
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 19
- 238000010791 quenching Methods 0.000 claims description 17
- 230000000171 quenching effect Effects 0.000 claims description 17
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 9
- 239000000126 substance Substances 0.000 claims description 8
- 238000001816 cooling Methods 0.000 claims description 6
- 238000005266 casting Methods 0.000 claims description 5
- 239000002826 coolant Substances 0.000 claims 1
- 238000004519 manufacturing process Methods 0.000 abstract description 7
- 238000009749 continuous casting Methods 0.000 abstract description 6
- 230000007797 corrosion Effects 0.000 abstract description 5
- 238000005260 corrosion Methods 0.000 abstract description 5
- 230000009286 beneficial effect Effects 0.000 abstract description 4
- 239000013078 crystal Substances 0.000 abstract description 4
- 238000005516 engineering process Methods 0.000 abstract description 2
- 238000005496 tempering Methods 0.000 abstract description 2
- 238000013461 design Methods 0.000 description 10
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 10
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 8
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 6
- 229910001566 austenite Inorganic materials 0.000 description 6
- 230000001976 improved effect Effects 0.000 description 6
- 239000010703 silicon Substances 0.000 description 6
- 238000000137 annealing Methods 0.000 description 5
- 239000000470 constituent Substances 0.000 description 5
- 230000009466 transformation Effects 0.000 description 5
- 239000005864 Sulphur Substances 0.000 description 4
- 230000007423 decrease Effects 0.000 description 4
- 238000012545 processing Methods 0.000 description 4
- 230000000717 retained effect Effects 0.000 description 4
- 238000003466 welding Methods 0.000 description 4
- 229910000859 α-Fe Inorganic materials 0.000 description 4
- 229910001563 bainite Inorganic materials 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000009628 steelmaking Methods 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- QFGIVKNKFPCKAW-UHFFFAOYSA-N [Mn].[C] Chemical compound [Mn].[C] QFGIVKNKFPCKAW-UHFFFAOYSA-N 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 230000007812 deficiency Effects 0.000 description 2
- 238000007872 degassing Methods 0.000 description 2
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N iron oxide Inorganic materials [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 238000011160 research Methods 0.000 description 2
- 230000003068 static effect Effects 0.000 description 2
- 239000011593 sulfur 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
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- 229910000677 High-carbon steel Inorganic materials 0.000 description 1
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- 241001062472 Stokellia anisodon Species 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 239000000571 coke Substances 0.000 description 1
- 238000006477 desulfuration reaction Methods 0.000 description 1
- 230000023556 desulfurization Effects 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000009510 drug design Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 238000009851 ferrous metallurgy Methods 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 238000009413 insulation Methods 0.000 description 1
- GNVXPFBEZCSHQZ-UHFFFAOYSA-N iron(2+);sulfide Chemical compound [S-2].[Fe+2] GNVXPFBEZCSHQZ-UHFFFAOYSA-N 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 230000005389 magnetism Effects 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 230000000116 mitigating effect Effects 0.000 description 1
- 239000011733 molybdenum Substances 0.000 description 1
- 150000004767 nitrides Chemical group 0.000 description 1
- 150000002829 nitrogen Chemical class 0.000 description 1
- 239000003921 oil Substances 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 229920001296 polysiloxane Polymers 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 238000003786 synthesis reaction Methods 0.000 description 1
- 238000000844 transformation Methods 0.000 description 1
- 239000002699 waste material 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
- 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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- 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
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—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
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
-
- 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
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The present invention relates to a kind of martensitic matrix 1100MPa grades of rare earths Q&P steel Preparation Method, ingredient is C:0.15~0.22%, Si:0.60~1.70%, Mn:1.10~2.40%, Mo:0.1~0.5%, Al:0.1~0.5%, V:0.05~0.11%, Y:0.01~0.05%, P:0.02~0.04%, S≤0.005%, Nb:0.040~0.0700%, N≤0.0060%, B:0.001~0.006%, surplus are Fe and inevitable impurity.Through converter smelting after ingredient, vacuum drying oven refining, continuous casting obtain slab, after trace alloying element powder is added in arc-melting furnace, obtain secondary slab, hot rolling after heating；Cold rolling after pickling；It is subsequently heated to coexistence region heat preservation；Carbon partition and tempering are finally organized.The present invention reduces the content of the elements such as C, Si, Mn in traditional steel grade by appropriate multiple beneficial alloying element, enhances weldability and corrosion resistance, refines crystal grain, and the steel plate of production has good comprehensive mechanical property, is conducive to automotive light weight technology and energy-saving and emission-reduction.
Description
Technical field
The present invention relates to a kind of Ferrous Metallurgy and manufacturing field, in particular to a kind of martensitic matrix 1100MPa grades of rare earths
Q&P steel Preparation Method.
Background technique
According to Ministry of Public Security's data, by the end of the year 2017, national vehicle guaranteeding organic quantity is up to 3.10 hundred million.It is handed in public security within 2017
33,520,000, motor vehicle of logical administrative department's new registration registration, record high.Car ownership was up to 2.17 hundred million, with 2016
It compares, whole year increases by 23,040,000, increases by 11.85%.The ratio that automobile accounts for motor vehicle is constantly improve, nearly 5 years accountings from
54.93% improves to 70.17%, it has also become motor vehicle constitutes main body.Meanwhile correlation test shows the every mitigation of the quality of automobile
10%, oil consumption can decline 6% ~ 8%, while discharge amount decline 4%.
Currently, China's although continuous 9 years acquisition world car sales volumes first, but the equal car ownership of thousand people just 140,
It differs greatly with developed country, still there is huge space.Therefore to advanced high-strength steel, more stringent requirements are proposed.Advanced high-strength steel
The effect of phase transformation strengthening has then been given full play on the basis of traditional reinforcing means, while having been cooperated with heat treatment process hand appropriate
Section obtains the heterogeneous structure containing martensite, bainite, ferrite and the two-phase of retained austenite or more so that each phase
Tissue gives full play to own characteristic, and respective disadvantage or deficiency is then weakened or is eliminated due to the presence of other phases, thus
Achieve the purpose that improve steel comprehensive performance.The representative advanced high-strength steel of research in recent years exploitation includes martensite (M)
Steel, two-phase (DP) steel, phase change induction plasticity (TRIP) steel, carbide-free Bainite/martensite complex phase (CFB/M) steel, twin lure
Send out plasticity (TWIP) steel and nanometer bainite (B) steel etc..Q&P steel is as the advanced high-strength steel quilt with favorable comprehensive mechanical property
Extensive concern and research.
Existing Q&P steel production technology has the problem that (1) is mostly to quench after existing steel grade is carried out full annealing
Fire-partition processing, i.e. material can pass through complete austenitizing twice, on the one hand will cause great energy waste, on the other hand
The a large amount of time can be also wasted during full annealing；(2) cost is reduced, only by the content of regulation C element, and benefit
Simply tissue adjustment is carried out with Mn, Si element.But excessively high C element content can seriously affect while increasing brittleness
Welding performance；(3) part high-strength steel has only focused on intensity or plasticity, and strength and ductility product is lower, is unable to satisfy the demand of Hyundai Motor；
(4) heat treatment process is complicated, and manufacturing requirements is higher, realizes the new instrument that industrialization needs buying price high, equipment
Management service cost is also relatively high.
Summary of the invention
In order to improve and solve above-mentioned deficiency, the present invention by the rational design to steel primitive component and treatment process,
A kind of martensitic matrix 1100MPa grades of rare earths Q&P steel Preparation Method is provided, comprehensive mechanical property can be greatly improved, reduces technique
Step is energy saving, has the characteristics of at low cost, high production efficiency.
To achieve the goals above, the technical solution that the present invention takes are as follows:
Present component design is as follows: C:0 .15~0 .22%, Si:0 .60~1 .70%, Mn:1 .10~2 .40%, Mo:
0.1~0.5%, Al:0 .1~0 .5%, V:0.05~0.11%, Y:0.01~0.05%, the P:0 .04% of .02~0, S≤0
.005%, Nb:0 .040~0 .0700%, N≤0 .0060%, B:0.001~0.006%, surplus be Fe and inevitably it is miscellaneous
Matter.
Ingredient design principle is as follows:
C: phosphorus content is higher, and the hardness and strength of steel are higher, but its poorer of plasticity and toughness is more than when carbon amounts
When 0.23%, the welding performance of steel will appear significant decline, while the raising of carbon amounts can also reduce the atmospheric corrosion resistance energy of steel
Power, outdoor stock ground high-carbon steel with regard to easy-to-rust；In addition, carbon can increase the cold brittleness and aging sensitivity of steel.Therefore, of the invention
The C element content of design is the .22% of 0 .15~0；
Si: the element in steel is added as deoxidier when being steel-making for silicon.FeO in silicon and molten steel can form the lesser silicon of density
Hydrochlorate clinker and be removed, therefore silicon is a kind of beneficial element.Silicon is dissolved in ferrite the intensity for making steel in steel, hardness increases
Add, plasticity, toughness reduce.Silicon can significantly improve the elastic limit of steel, yield point and tensile strength.Since silicone content does not surpass in steel
When 0.5%, Steel Properties are influenced less, therefore the Si constituent content that the present invention designs is the .70% of 0 .60~1；
Mn: it is added in steel when manganese is steel-making as deoxidier.Since manganese can form the MnS of high-melting-point (1600 DEG C) with sulphur,
The illeffects of sulphur is eliminated to a certain extent.Manganese has good deoxidizing capacity, can enter with the FeO in steel as MnO
Clinker especially reduces the brittleness of steel, improves the intensity and hardness of steel so as to improve the quality of steel.Therefore, manganese is one in steel
Kind beneficial element, can effectively improve the quenching property of steel, improve the hot-working character of steel when being added 0.70% or more.But manganese amount
It is excessively high, weaken the resistance to corrosion of steel, reduces welding performance, therefore the Mn constituent content that the present invention designs is 1 .10~2
.40%；
Mo: can significantly improve the harden ability and heat resistance of steel, prevent temper brittleness, improve remanent magnetism and coercivity, make the crystalline substance of steel
Grain refinement, keeps enough intensity and creep resisting ability at high temperature.Molybdenum is added in steel, mechanical performance can be improved, can also press down
Alloyage steel brittleness due to caused by tempering, can also promote resistance to corrosion, therefore, what the present invention designed to a certain extent
Mo constituent content is 0.1~0.5%；
Al: can refine the grain structure of steel, suppress the timeliness of mild steel to improve the toughness of steel at low temperature, moreover it is possible to improve steel
Inoxidizability improves wearability and fatigue strength of steel etc..Therefore, the Al constituent content that the present invention designs is 0.1~0.5%；
V: Grain refinement is strong, and the intensity and toughness of steel can be improved, and reduces superheated susceptivity, improves thermal stability.Improve M body
Temper resistance.The spread of general VC is very high and extremely stable.So can be with deoxidation, degassing.Fine and close fine grained texture is obtained,
Plasticity, toughness and high intensity are improved, impact property and fatigue strength are all high compared with no V steel, have in high temperature and low temperature (0 DEG C of <)
High-intensitive, toughness.Since the high degree of dispersion of vanadium carbide prevents weld grain coarse, so the solderability of steel can be improved, but add
It can cause steel is brilliant to grow up strongly after heat to VC solution temperature, therefore the V element content that the present invention designs is 0.05~0.11%；
Y: having degassing, desulfurization and eliminates the effect of other objectionable impurities, improves the as-cast structure of steel, antioxygen can be improved in extremely low content
The property changed, elevated temperature strength and creep strength increase corrosion resistance, and therefore, the Y element content that the present invention designs is 0.01~0.05%；
N: the ability of ferrite dissolved nitrogen is very low.When in steel dissolved with oversaturated nitrogen, after placing longer period of time or then
Nitrogen will occur with the precipitation of nitride form in 200~300 DEG C of heating, and improve the hardness of steel, intensity, plasticity decline,
Timeliness occurs.Al, Ti or V are added in molten steel and carries out fixed nitrogen processing, is fixed on nitrogen in AlN, TiN or VN, timeliness can be eliminated and inclined
To.Therefore the N element content that the present invention designs is 0 .006%；
S: ore and fuel coke of the sulphur from steel-making.It is one of steel harmful element.Sulphur is with the shape of iron sulfide (FeS)
State is present in steel, and FeS and Fe form low melting point (985 DEG C) compound.And the hot processing temperature of steel generally 1150~
1200 DEG C or more, so when steel hot-working, due to FeS compound too early fusing and cause workpiece to crack, this phenomenon
Referred to as " hot-short ".Sulfur content is higher, and hot-short phenomenon is more serious, therefore must control sulfur content in steel.Therefore the present invention is set
The S constituent content of meter is≤0 .005%；
B: when containing micro (0.001-0.005 %) boron in steel, the harden ability of steel can be increased exponentially, right at this time
Other performance etc. is very small without influencing or influencing, but when amount containing B is more than 0.007%, easily causes brittleness, and therefore, the present invention designs
B element content be 0.001~0.006%.
A kind of martensitic matrix 1100MPa grades of rare earths Q&P steel Preparation Method, its step are as follows:
(1) smelting process: according to component prescription given by the present invention, by converter smelting after ingredient, vacuum drying oven double refining,
Continuous casting obtains slab, the chemical component and weight percentage of the slab are as follows: .60~1 C:0 .15~0 .22%, Si:0
.70%, Mn:1 .10~2 .40%, Mo:0.1~0.5%, Al:0 .1~0 .5%, P:0 .02~0 .005% of .04%, S≤0,
The .0060% of N≤0, surplus are Fe and inevitable impurity；
(2) microelement fuses into process: trace alloying element powder being added in arc-melting furnace, obtains secondary slab, gained
The nearly weight percent content of the chemical component of slab are as follows: .10~2 C:0 .15~0 .22%, Si:0 .60~1 .70%, Mn:1
.40%, Mo:0.1~0.5%, Al:0 .1~0 .5%, V:0.05~0.11%, Y:0.01~0.05%, the P:0 .04% of .02~0,
S≤0 .005%, the Nb:0 .0060% of .0700%, N≤0 of .040~0, B:0.001~0.006%, surplus is for Fe and unavoidably
Impurity；
(3) course of hot rolling: slab is heated to 1100-1150 DEG C using heating furnace and is carried out heat preservation a period of time, is then carried out
Hot rolling, rear water quenching to room temperature；
(4) cold-rolled process: multi-pass cold rolling is carried out after pickling, obtains the steel plate of target thickness；
(5) material two-phase section manganese partition process: is heated to A with given paceC3And AC1It a certain temperature and is protected between (coexistence region)
Water quenching is to room temperature after warm a period of time；
(6) carbon partition processes: by material in MSWith MfBetween a certain temperature T0Carry out heat preservation a period of time, after by material water
It quenches to room temperature；
(7) secondary carbon partition process: by material in MSWith MfBetween a certain temperature T1(T1Temperature ratio T0It is slightly lower) carry out one section of heat preservation
Time, after by material water quenching to room temperature.
Casting process uses in the step of described a kind of martensitic matrix 1100MPa grades of rare earths Q&P steel Preparation Method (1)
Continuous casting process；
Alloy powder main component in the step of described a kind of martensitic matrix 1100MPa grades of rare earths Q&P steel Preparation Method (2)
For Mo, Al, V, Y, Nb, N, B；
Finishing temperature is 820- in the step of described a kind of martensitic matrix 1100MPa grades of rare earths Q&P steel Preparation Method (3)
880 DEG C, 550-650 DEG C of coiling temperature, steel plate thickness obtained is 1.8-2.0mm；
Cold rolling steel plate obtained in the step of described a kind of martensitic matrix 1100MPa grades of rare earths Q&P steel Preparation Method (4)
With a thickness of 1.2-1.5mm, it is preferred that acid pickling step is as follows: first step pickling → flowing water washes → and second step pickling → flowing water washes →
It is transferred to next procedure；
A in the step of described a kind of martensitic matrix 1100MPa grades of rare earths Q&P steel Preparation Method (5)C3And AC1By thermally expanding
Instrument test obtains and takes into account error；
Cooling in a kind of the step of described martensitic matrix 1100MPa grades of rare earths Q&P steel Preparation Method (5) (6) (7) step
The static CCT curve (one temperature curve of swell increment) that rate is measured by thermal dilatometer determines, available by static CCT curve
The critical cooling rate of martensitic traoformation；
Heat preservation a period of time in the step of described a kind of martensitic matrix 1100MPa grades of rare earths Q&P steel Preparation Method (6) (7)
For 10 ~ 300 s.
Beneficial effects of the present invention are as follows:
(1) it under rolling and quenching state, directly carries out Q&P technique after cold rolling, rather than general first carries out a full annealing
Obtain the tissue based on pearlite.Cancel a step full annealing, on the one hand save the energy, on the other hand eliminates annealing cooling
Fall into a long wait；
(2) suitable trace alloying element is added, on the one hand promotes crystal grain refinement, enhances the synthesis of steel plate using refined crystalline strengthening
Mechanical property；On the other hand carbon manganese element content is reduced, reduces the welding difficulty of steel plate；
(3) by Martensitic Transformation twice, crystal grain is cut, achievees the effect that crystal grain refinement, while promoting the distribution of C element
Process and the stability for strengthening retained austenite；
(4) continuous casting process is used, cooling velocity is fast, continuous throwing, casting condition is controllable, stablizes, therefore casting blank inner organization is equal
Even, fine and close, reduced in segregation, performance are also stable；
(5) using carbon partition twice, carbon is made to obtain sufficient utilization, substantially stabilized retained austenite obtains good comprehensive
Close mechanical property.
Detailed description of the invention
Fig. 1 is heat treatment process flow chart of the present invention.
Fig. 2 is the metallographic structure photo of the embodiment of the present invention 1.
In figure, 1, smelt fusion-casting process, 2, trace alloying element fuse into process, 3, heating and thermal insulation process, 4, course of hot rolling,
5, cold-rolled process, 6, the comprehensive partition of coexistence region carbon manganese, 7, carbon partition processes, 8, secondary carbon partition process, 9, AC3Line represents
Ferritic transformation is the finishing temperature of austenite, 10, A when heatingC1Line represent heating when perlitic transformation as austenite temperature,
11、MfLine indicates martensite transfor mation finishing temperature, 12, MSLine indicates that geneva changes start temperature.
Specific embodiment:
Specific embodiment is described in detail with reference to the accompanying drawings and examples, as shown in attached drawing 1-2.
Metallographic specimen in the embodiment of the present invention shoots under an optical microscope and obtains microstructure photo；Tensile sample
It is made according to ASTME8 standard, and using WDW-100E type electronic universal tester at room temperature with the rate of extension of 1mm/min
Extension test is carried out, after tested and calculates tensile strength, elongation after fracture and the strength and ductility product for obtaining each sample.
Embodiment 1
The material composition and weight percent used in actual production is C:0 .18%, Si:0 .80%, Mn:1 .70%, Mo:
0.30%, Al:0 .20%, V:0.05%, Y:0.01%, P:0 .02%, S≤0 .005%, Nb:0 .040%, N≤0 .0060%, B:
0.001%, surplus is that Fe and inevitable impurity, technical process comprise the following steps:
(1) smelting process: according to component prescription given by the present invention, by converter smelting after ingredient, vacuum drying oven double refining,
Continuous casting obtains slab, the chemical component and weight percentage of the slab are as follows: C:0 .18%, Si:0 .80%, Mn:1 .70%,
Mo:0.30%, Al:0 .20%, the P:0 .0060% of .005%, N≤0 of .02%, S≤0, surplus are Fe and inevitable impurity；
(2) microelement fuses into process: trace alloying element powder being added in arc-melting furnace, obtains secondary slab, gained
The nearly weight percent content of the chemical component of slab are as follows: C:0 .18%, Si:0 .80%, Mn:1 .70%, Mo:0.30%, Al:0
.20%, V:0.05%, Y:0.01%, P:0 .02%, S≤0 .005%, Nb:0 .040%, N≤0 .0060%, B:0.001%, surplus
For Fe and inevitable impurity；
(3) course of hot rolling: slab is heated to 1100 DEG C using heating furnace and carries out 1.5 h of heat preservation, then carries out hot rolling, finish to gauge
Temperature is 860 DEG C, and 650 DEG C of steel plate thickness of coiling temperature are 1.8mm, rear water quenching to room temperature；
(4) cold-rolled process: carrying out six passage cold rollings after pickling, obtains 1.2 mm steel plate of target thickness；
(5) two-phase section manganese partition process: water quenching after material is heated to 770 DEG C and 200 s of heat preservation with 10 DEG C of rates per minute
To room temperature；
(6) carbon partition processes: being heated to 300 DEG C for material with 10 DEG C of rates per minute and keep the temperature 120 s, after by material
Water quenching is to room temperature；
(7) secondary carbon partition process: being heated to 280 DEG C for material with 10 DEG C of rates per minute and keep the temperature 90 s, after by material
Water quenching is to room temperature.
Fig. 2 is metallurgical tissue picture, and tissue is by martensite, granular ferrite and retained austenite group after can determine whether processing
At.Elongation after fracture reaches 21.08 %, 1141.06 MPa of tensile strength, 23.9 GPa% of strength and ductility product.
Embodiment 2
The material composition and weight percent used in actual production is C:0 .18%, Si:1 .10%, Mn:1 .90%, Mo:
0.1%, Al:0 .18%, V:0.05%, Y:0.02%, P:0 .03%, S≤0 .005%, Nb:0 .050%, N≤0 .0060%, B:
0.001%, surplus is that Fe and inevitable impurity, technical process comprise the following steps:
(1) smelting process: according to component prescription given by the present invention, by converter smelting after ingredient, vacuum drying oven double refining,
Continuous casting obtains slab, the chemical component and weight percentage of the slab are as follows: C:0 .18%, Si:1 .10%, Mn:1 .90%,
Mo:0.1%, Al:0 .18%, the P:0 .0060% of .005%, N≤0 of .03%, S≤0, surplus are Fe and inevitable impurity；
(2) microelement fuses into process: trace alloying element powder being added in arc-melting furnace, obtains secondary slab, gained
The nearly weight percent content of the chemical component of slab are as follows: C:0 .18%, Si:1 .10%, Mn:1 .90%, Mo:0.1%, Al:0
.18%, V:0.05%, Y:0.02%, P:0 .03%, S≤0 .005%, Nb:0 .050%, N≤0 .0060%, B:0.001%, surplus
For Fe and inevitable impurity；
(3) course of hot rolling: being heated to 1100 DEG C using heating furnace for slab and carry out 100 min of heat preservation, then carry out hot rolling,
Finishing temperature is 860 DEG C, and 680 DEG C of steel plate thickness of coiling temperature are 1.8mm, rear water quenching to room temperature；
(4) cold-rolled process: carrying out six passage cold rollings after pickling, obtains 1.2 mm steel plate of target thickness；
(5) two-phase section manganese partition process: water quenching after material is heated to 780 DEG C and 200 s of heat preservation with 10 DEG C of rates per minute
To room temperature；
(6) carbon partition processes: being heated to 280 DEG C for material with 10 DEG C of rates per minute and keep the temperature 60 s, after by material
Water quenching is to room temperature；
(7) secondary carbon partition process: being heated to 260 DEG C for material with 10 DEG C of rates per minute and keep the temperature 40 s, after by material
Water quenching is to room temperature.
Elongation after fracture reaches 20.38 %, 1180.06 MPa of tensile strength, 24.0 GPa% of strength and ductility product.
Claims (4)
1. a kind of martensitic matrix 1100MPa grades of rare earths Q&P steel Preparation Method, it is characterised in that the nearly weight percent of chemical component
Content are as follows: C:0.15~0.22%, Si:0.60~1.70%, Mn:1.10~2.40%, Mo:0.1~0.5%, Al:0.1~0.5%,
V:0.05~0.11%, Y:0.01~0.05%, P:0.02~0.04%, S≤0.005%, the Nb:0 .0700% of .040~0, N≤0
.0060%, B:0.001~0.006%, surplus are Fe and inevitable impurity.
2. a kind of martensitic matrix 1100MPa grades of rare earths Q&P steel Preparation Method described in claim 1, it is characterised in that specific
Preparation step is as follows:
(1) smelting process: according to component prescription given by the present invention, by converter smelting after ingredient, vacuum drying oven double refining,
Casting obtains slab；
(2) microelement fuses into process: trace alloying element powder (Mo, Al, V, Y, Nb, N, B being added in arc-melting furnace
Deng), obtain secondary slab；
(3) course of hot rolling: slab is heated to 1100-1150 DEG C using heating furnace and carries out heat preservation 1-3 h, then carries out heat
It rolls, finishing temperature is 820-880 DEG C, and 550-650 DEG C of coiling temperature, steel plate thickness obtained is 1.5-3.0mm, and rear water quenching is arrived
Room temperature；
(4) cold-rolled process: carrying out multi-pass cold rolling after pickling, obtains the steel plate with a thickness of 1.2-1.5mm；
(5) material two-phase section manganese partition process: is heated to A with 10-30 DEG C/sC3And AC1It a certain temperature and is protected between (coexistence region)
Water quenching is to room temperature after warm 3-15 min；
(6) carbon partition processes: by material in MSWith MfBetween a certain temperature T0Carry out heat preservation 10-300 s, after by material water
It quenches to room temperature；
(7) secondary carbon partition process: by material in MSWith MfBetween a certain temperature T1(T1Temperature ratio T0It is slightly lower) 10-300 s is carried out,
Afterwards by material water quenching to room temperature.
3. a kind of martensitic matrix 1100MPa grades of rare earths Q&P steel Preparation Method described according to claim 1, it is characterized in that: institute
State by material water quenching to room temperature, cooling rate and cooling medium used have the martensite critical cooling rate institute of specific material
It determines.
4. a kind of martensitic matrix 1100MPa grades of rare earths Q&P steel Preparation Method described according to claim 1, it is characterized in that: institute
State by material, carbon partition first time temperature is slightly higher with secondary temperature twice.
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| CN110093559A (en) * | 2019-04-25 | 2019-08-06 | 西南大学 | Steel splitting plate and preparation method are matched in quenching-tempering based on carbon manganese collaboration partition |
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| CN110093559A (en) * | 2019-04-25 | 2019-08-06 | 西南大学 | Steel splitting plate and preparation method are matched in quenching-tempering based on carbon manganese collaboration partition |
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| WO2024244041A1 (en) * | 2023-05-30 | 2024-12-05 | 鞍钢股份有限公司 | Quenched and partitioned steel for automobiles and gradient partitioning preparation method therefor |
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