CN103649355B - Have the HAZ-of improvement soften repellence hot-rolled high-strength steel band and the method that produces described steel - Google Patents
Have the HAZ-of improvement soften repellence hot-rolled high-strength steel band and the method that produces described steel Download PDFInfo
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- CN103649355B CN103649355B CN201280034223.9A CN201280034223A CN103649355B CN 103649355 B CN103649355 B CN 103649355B CN 201280034223 A CN201280034223 A CN 201280034223A CN 103649355 B CN103649355 B CN 103649355B
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- 230000006872 improvement Effects 0.000 title claims abstract description 7
- 229910000831 Steel Inorganic materials 0.000 title claims description 86
- 239000010959 steel Substances 0.000 title claims description 86
- 238000000034 method Methods 0.000 title claims description 16
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 30
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 19
- 229910000742 Microalloyed steel Inorganic materials 0.000 claims abstract 4
- 229910052799 carbon Inorganic materials 0.000 claims description 22
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 18
- 239000010955 niobium Substances 0.000 claims description 17
- 238000005096 rolling process Methods 0.000 claims description 16
- 238000005098 hot rolling Methods 0.000 claims description 13
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 12
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 12
- 239000010949 copper Substances 0.000 claims description 11
- 239000012535 impurity Substances 0.000 claims description 11
- 239000011575 calcium Substances 0.000 claims description 10
- 239000010936 titanium Substances 0.000 claims description 10
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 claims description 8
- 238000001816 cooling Methods 0.000 claims description 8
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 claims description 7
- 229910052791 calcium Inorganic materials 0.000 claims description 7
- 229910052758 niobium Inorganic materials 0.000 claims description 7
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 6
- 230000008859 change Effects 0.000 claims description 6
- 229910052802 copper Inorganic materials 0.000 claims description 6
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 5
- 238000004519 manufacturing process Methods 0.000 claims description 4
- 229910052759 nickel Inorganic materials 0.000 claims description 3
- 229910001566 austenite Inorganic materials 0.000 description 13
- 239000000203 mixture Substances 0.000 description 13
- 238000003466 welding Methods 0.000 description 13
- 230000000694 effects Effects 0.000 description 11
- 229910052796 boron Inorganic materials 0.000 description 10
- 239000000463 material Substances 0.000 description 10
- 229910000859 α-Fe Inorganic materials 0.000 description 10
- 229910052782 aluminium Inorganic materials 0.000 description 9
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 8
- 229910052750 molybdenum Inorganic materials 0.000 description 8
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 7
- 238000001556 precipitation Methods 0.000 description 7
- 239000011651 chromium Substances 0.000 description 6
- 239000013078 crystal Substances 0.000 description 6
- 238000005520 cutting process Methods 0.000 description 6
- 239000011572 manganese Substances 0.000 description 6
- 238000005496 tempering Methods 0.000 description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 4
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 4
- 238000005275 alloying Methods 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 4
- 229910052804 chromium Inorganic materials 0.000 description 4
- 238000005516 engineering process Methods 0.000 description 4
- 229910052748 manganese Inorganic materials 0.000 description 4
- 239000011733 molybdenum Substances 0.000 description 4
- 230000008569 process Effects 0.000 description 4
- 229910052710 silicon Inorganic materials 0.000 description 4
- 229910052719 titanium Inorganic materials 0.000 description 4
- PNEYBMLMFCGWSK-UHFFFAOYSA-N Alumina Chemical compound [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 3
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 3
- 238000005266 casting Methods 0.000 description 3
- 238000009749 continuous casting Methods 0.000 description 3
- 229910052757 nitrogen Inorganic materials 0.000 description 3
- 238000002360 preparation method Methods 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 230000009467 reduction Effects 0.000 description 3
- 230000007704 transition Effects 0.000 description 3
- RMLPZKRPSQVRAB-UHFFFAOYSA-N tris(3-methylphenyl) phosphate Chemical compound CC1=CC=CC(OP(=O)(OC=2C=C(C)C=CC=2)OC=2C=C(C)C=CC=2)=C1 RMLPZKRPSQVRAB-UHFFFAOYSA-N 0.000 description 3
- 239000002023 wood Substances 0.000 description 3
- 229910052582 BN Inorganic materials 0.000 description 2
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 2
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 238000005452 bending Methods 0.000 description 2
- XFWJKVMFIVXPKK-UHFFFAOYSA-N calcium;oxido(oxo)alumane Chemical compound [Ca+2].[O-][Al]=O.[O-][Al]=O XFWJKVMFIVXPKK-UHFFFAOYSA-N 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 238000007731 hot pressing Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 239000010813 municipal solid waste Substances 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 229910001562 pearlite Inorganic materials 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 239000010703 silicon Substances 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- 229910000967 As alloy Inorganic materials 0.000 description 1
- 229910014460 Ca-Fe Inorganic materials 0.000 description 1
- 229910014458 Ca-Si Inorganic materials 0.000 description 1
- -1 Cr and Mo carbide Chemical class 0.000 description 1
- SLZWEMYSYKOWCG-UHFFFAOYSA-N Etacelasil Chemical compound COCCO[Si](CCCl)(OCCOC)OCCOC SLZWEMYSYKOWCG-UHFFFAOYSA-N 0.000 description 1
- 229910000655 Killed steel Inorganic materials 0.000 description 1
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- BPQQTUXANYXVAA-UHFFFAOYSA-N Orthosilicate Chemical compound [O-][Si]([O-])([O-])[O-] BPQQTUXANYXVAA-UHFFFAOYSA-N 0.000 description 1
- 208000031481 Pathologic Constriction Diseases 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- 208000037656 Respiratory Sounds Diseases 0.000 description 1
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 1
- 229910000746 Structural steel Inorganic materials 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- NRTOMJZYCJJWKI-UHFFFAOYSA-N Titanium nitride Chemical compound [Ti]#N NRTOMJZYCJJWKI-UHFFFAOYSA-N 0.000 description 1
- 230000001133 acceleration Effects 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- CSDREXVUYHZDNP-UHFFFAOYSA-N alumanylidynesilicon Chemical compound [Al].[Si] CSDREXVUYHZDNP-UHFFFAOYSA-N 0.000 description 1
- 239000004411 aluminium Substances 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 150000001721 carbon Chemical class 0.000 description 1
- 150000001722 carbon compounds Chemical class 0.000 description 1
- 210000005056 cell body Anatomy 0.000 description 1
- 229910052729 chemical element Inorganic materials 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 239000002537 cosmetic Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 239000008187 granular material Substances 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 238000003801 milling Methods 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 238000009377 nuclear transmutation Methods 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 229920001296 polysiloxane Polymers 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000003303 reheating Methods 0.000 description 1
- 235000015170 shellfish Nutrition 0.000 description 1
- 229910052814 silicon oxide Inorganic materials 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- 230000000930 thermomechanical effect Effects 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 210000001215 vagina Anatomy 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 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
- C22C38/04—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
- 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
- C21D2211/002—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
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 Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention provides have improvement HAZ soften repellence hot-rolled high-strength microalloy steel band, it has the microscopic structure comprising martensite, tempered martensite and/or bainite.
Description
The present invention relates to have the HAZ-of improvement soften repellence hot-rolled high-strength steel band and
The method producing described steel.
Traditionally, manufactured the steel with high-yield strength by austenitizing and quenching, but logical
Cross this technology, it may not be possible to realize surface quality and the impact flexibility such as optimized.Preparation expense
The highest.
EP1375694 describes to be produced by hot rolling has good processing characteristics and welding performance
High intensity, the method for high-ductility steel.But, the inventors discovered that these steel are prone to HAZ-and soften.
Heat affected area (HAZ) is for being changed its microscopic structure and character by welding or hot intensive cutting operation
The region of base material.Encirclement is result in from welding process and the heat cooled down again subsequently
Change in the region of this weld seam.The heat affected area forming the weld seam in this steel neighbouring is that welding is lost
One of most common region of effect.Modern thermo-mechanical rolling (TMCP) steel, lean due to them
Chemical composition, and low carbon content especially, it is therefore desirable to the welding parameter carefully controlled is to realize
Sufficient intensity in weld seam HAZ.For conventional mild steel and some TMCP pipe line steel, such as
X70 and X80, HAZ soften often owing to the high heat that in HAZ, heat dissipates slowly inputs
The result of welding sequence.For the TMCP steel of higher level, such as X100, due to substrate gold
The microscopic structure that the ultra fine grain size belonged to and its bainite and martensite are dominated, HAZ softens can
Even occur under medium welding heat inputs.Hardness and the reduction of intensity in HAZ are
The weak spot of welded pipeline configuration.Therefore, according to base material and the character of welding condition,
The degree limiting this softening generation is important.Leading by most research is softened about HAZ
Territory is high-strength medium plate, such as pipe applications, and closer to the phase for automobile application
AHSS。
WO2007/129676 relates to the hot pressing steel part manufactured by high-carbon cold-rolled steel sheet material, this steel
Sheet material by austenitizing, hot pressing to produce steel part and to be quenched realizing the minimum of 1.8GPa and draw
Stretch intensity.Treat the ferrite that cold rolling hot-rolled steel contains at least 50%.
EP2028284 discloses seamless steel pipe and EP1662014 discloses low-carbon hot-rolling steel board,
It batches between 450～650 DEG C and is heated again to the most rapidly between 550～750 DEG C
To realize three-phase ferrite, bainite and island martensite soma.
It is an object of the invention to realize high-strength hot-rolled steel band, it is more high-strength than now available
Degree hot-rolled steel band is less prone to HAZ-and softens.
At first aspect, by have the HAZ of improvement soften repellence hot-rolled high-strength micro-
The steel band of alloying has reached this purpose, its thickness having between 2～16mm, has bag
Containing the microscopic structure of martensite, tempered martensite and/or bainite, and wherein this steel with weight %
Meter contains:
● 0.07～the C of 0.30%；
● 0.8～the Mn of 2.0%；
● 0.01～the Al of 0.08%sol；
● 0.2～the Cr of 1.5%；
● 0.1～the Mo of 0.7%；
● the B of 0.0005～0.005；
● 0.01～the Nb of 0.07%；
● the Si of most 0.5%；
● the P of most 0.03%；
● the S of most 0.015%；
● the Ti of most 0.05%；
● the V of most 0.1%；
● the Cu of most 0.2%；
● the Ni of most 0.2%；
● the N of most 0.008%；
● the calcium interpolation controlled for sulphide shape of the most most 0.015%；
● being in other elements of the amount of impurity level, surplus is ferrum；
The yield strength of this steel band is at least 960MPa.
All of composition % is all given with weight %, unless otherwise specified.
Thinking of the present invention based on the fact that, by the combination of chemical element of the amount described in selecting,
And particularly niobium and the existence of molybdenum, good hardening can be kept.Due to low manganese and carbon content,
During casting process, structure of steel is not critical for the segregation of manganese and carbon.This rigidity is verified in band
The local relief of the coiling temperature in material is not critical, and which promotes steel and produces, and to its machinery
The uniformity of character has advantageous effect, this flatness and residual stress to final products again
There is active influence.This steel sheets height is suitable for welding and cut, and it has simultaneously
Good fatigue strength, not by described Effects of Heat Treatment.And, this steel sheets has excellence
Bending property, good impact flexibility and tempering time to soften good repellence.Subsequently,
Precipitation element in the cooling period obtainable solution for separating out of HAZ after being welded
Existence ensure that HAZ soften repellence be obviously improved.
Can be such as the shape accurately defined by laser by the steel thermal cutting according to the present invention.?
Observe in cut article, achieve notable smooth cutting surfaces.On the other hand,
Find that the strength difference between base material and the soft zone produced in the cutting process of technology (should
Region is located close to hardening zone) it is little or non-existent, this is also due to after this thermal cutting
Cooling period the most obtainable for separate out solution in separate out element existence.This
Jointly fatigue strength had favorable influence a bit.Additionally, relatively low carbon content reduces firmly
Change the peak hardness in district so that no matter at the processing of article or this cutting table in actual use
In the face of brittle insensitive with cracking.
In terms of controlling intensity, carbon is important element, but needs to be not limited to a certain degree
To provide the well balanced of toughness, welding performance and processability.This C content is remained phase
To between low 0.07～0.30%, to realize good toughness, (all of composition % is all with weight %
Represent).Being combined with low temperature coiling temperature, this microscopic structure will be containing martensite and/or bainite.
Definite amount depends strongly on composition, cooldown rate on the run-out table and coiling temperature.?
Under relatively low C content, this Ms temperature is by a relatively high, and therefore, martensite will be to a certain degree
Upper self tempering.According to requirement of strength, it was found that suitably carbon window.For having at least 960MPa
The steel of yield strength, preferably carbon content is at least 0.07 and/or most 0.13%.For tool
Having the steel of the yield strength of at least 1100MPa, carbon content is preferably at least 0.13 and/or at most
0.18%, and for having the steel of the yield strength of at least 1300MPa, carbon content is preferably at least
0.19%, between more preferably at least 0.23 and/or most 0.30%.
Suitably greatest carbon content is 0.27%, or even 0.25%.
As manganese, chromium, molybdenum and the element of boron, it is provided that promote bainite and/or the formation of martensite
Hardenability.This Fe content is limited to 0.8～2.0%.When manganese exceedes this upper limit, segregation
Risk becomes obvious, and this can deleteriously affect the uniformity of microscopic structure.Water less than 0.8%
At ordinary times, the effect to hardenability is insufficient.The most minimum manganese level is 1.1%.
Add boron to promote hardenability.The formation avoiding boron nitride is important, because it will
Make boron invalid for the raising of hardenability.According to the titanium in the compositions of the present invention act as protect
Protect boron, because Ti forms titanium nitride, and be therefore formed without BN.The amount of the boron of alloying
It is at least 0.0005%B (i.e. 5ppm), but less than 0.005%B (i.e. 50ppm) to reduce crystal grain
Size and raising hardenability.If adding titanium to be generally at least as alloy element, the amount of titanium
0.01%Ti, but less than 0.05%, to combine nitrogen N and to prevent the generation of boron nitride BN.
Within the scope of the invention alternative for using aluminum to combine nitrogen, and thus protects boron.At TiN
The formation of granule is considered need not the situation of (such as because of they effects to Charpy toughness)
Under, can be preferably to select by the boron that aluminum protection is free.
During hot rolling, niobium analyzes in the middle part of austenite, from there through the recrystallization of austenite
Retardation the crystal grain refinement of the final microscopic structure changed is had contribution.Additionally, protect on the turn
Stay the niobium in solution, particularly under cooldown rate faster, reduction transition temperature is had and have
The effect of power, therefore it is also advantageous for hardenability.(＜ at a low coiling temperature
500 DEG C), it is contemplated that niobium is little by the contribution of precipitation strength, because this temperature is for thin NbC
Precipitation the lowest.Suitably Nb content is at least 0.02%, preferably at least 0.025%.
In this case, V has the effect similar but the strongest with Nb.But, Nb
The main cause of the interpolation with V is to improve HAZ-to soften repellence.In the relevant portion of HAZ,
Thermal cycle makes the temperature having reached to allow the precipitation strength by Nb and V, therefore result in hard
The increase of degree, this is due to the precipitation of the element being maintained in solution by low coiling temperature.
It is believed that main contribution is produced by Nb and V carbide, nitride or carbonitride.?
In lower degree, it is believed that the MoC precipitate with similar effect can be formed.If it does, close
Suitable minimum V content is 0.04%.
Steel according to the present invention is aluminium deoxidation or aluminum-silicon killed steel, so that oxygen content is down to minima,
Not react between carbon and oxygen during solidifying.The aluminum to steel is added at production period
Amount therefore include needing for those of deoxidation.The amount kept in the final product is (also referred to as
Solvable aluminum (Alsol)) it is 0.01～0.08%Al.In the context of the present invention, aluminum content
Mean solvable aluminum.
Except aluminum, silicon also functions as deoxidizer in the steel of the present invention.It starts from the most at least 0.10%Si
And at most 0.50%Si also functions as solution strengthening thing, this On Impact Toughness and processing characteristics have and have
The effect of benefit.Higher than 0.5%, silicon deleteriously affects the surface quality extremely unacceptable degree of steel,
And along with the silicone content increased, become more difficult by the removal of the hot rolling iron scale of pickling.
The phosphorus P being included as impurity should be most 0.03%, and sulfur S should be even lower,
And most 0.015% should be defined as, it means that limit these content to realize good impact
Toughness and bending property.As necessary, by using the band containing Ca-Si or Ca-Fe (Ni)
Core welding wire processes this melt can improve further performance.During Calcium treatment, owing to surface is opened
Power effect, aluminium oxide and silicon oxide field trash be converted into melted spherical form calcium-aluminate and
Silicate.Staying the calcium-aluminate field trash in molten steel inhibits MnS to send out during the solidification of steel
The formation of stricture of vagina (stringer).The composition of precipitation of Sulfide inclusion and mould during steel solidification
This change in terms of formula is referred to as oxide morphology or sulphide shape controls.Which results in casting
Make period less spray nozzle clogging, preferable mechanical performance, because the long MnS hairline stretched fills
When crackle produces point.The general quantity of calcium in the steel that sulphide shape controls be 0.0015～
The Ca of 0.015%.Suitably maximum is the Ca of 0.005%.
Chromium should be 0.2～1.5%.Molybdenum should preferably last 0.1%Mo～0.7%Mo.Add two
Plant element to improve hardening and tempering repellence.This makes the precipitation under higher coiling temperature become
For may, can use it for reducing and even preventing the softening of steel, and be used for alleviating due to
The intensity fluctuation that the cooling period of coiled material causes owing to local temperature difference is different.The most minimum molybdenum contains
Amount is 0.15%.
In view of the cosmetic issue relevant to copper, preferably avoid and be frequently used for this intensity level
Element in steel such as copper and mickel alloying.Because often copper is combined nickel carries out alloying to subtract
The adverse effect of light copper, so this is also needs.Therefore preferably nickel and/or copper is with most impurity
Level exists or is more preferably completely absent.
The microscopic structure of the steel according to the present invention is characterized as being mainly by showing that tempered martensite forms
Micro-assembly robot, it is characterised in that the little carbide in Widmannstatten structure and/or bainite.It is desirable that
This microscopic structure does not contains ferrite and pearlite composition, because these will deleteriously affect to be achieved
Intensity level.It practice, the ferrite that there are some small pieces may is that inevitably, but
This amount can be less than the level significantly affecting intensity level.Should will be formed under high transition temperature
Above-described harmful and the most unwanted ferrite composition and shape under low transition temperature
The ferritic portion of the bainite become or ferrite side plate or acicular ferrite understand separately.
The former composition is unwanted, and the latter is not.
Can the hot-rolled steel band being directly hot-rolled down to the present invention of 2mm～16mm thickness be prepared as resistance to
Grind and there is different SMYSs.Only by within the scope of the invention change analyze and/
Or the rear rolling cooldown rate of band and/or the temperature before batching, the most general threshold value
It is 960,1100 and 1300MPa.Also this kind of high yield stress steel can be used in target, at this
The performance that in target, organization need structural steel is generally required, the best processing characteristics, welding
Performance and impact flexibility, it means that according to the hot-rolled steel band of the present invention as welding knot
Structure steel also can shape.During the steel that will be explained in the following description is analyzed, all of
Content % is weight %, and the surplus of steel is ferrum Fe and inevitable impurity, unless otherwise limit
Fixed.One-tenth-value thickness 1/10 even for the tropocal wood of at most 16mm, it is possible to reach the value of 960MPa.
For the value of at most 12mm, can reach the value of 1100 and 1300MPa.Higher thickness is at certain
Result in relatively low cooldown rate in kind of degree, and therefore result in before phase in version less
The austenite of enrichment.This causes the intensity level that some is relatively low, it is meant that use these lean compositions,
S1100 or S1300 level can not be obtained for the thickness tropocal wood more than 12mm.Preferably,
Minimum thickness is 3mm and/or maximum gauge is 10mm.It should be noted that as defined in the present invention
Intensity level be measure in a longitudinal direction (i.e. tensile sample is on the longitudinal direction of this band
(by the direction of motion of milling train) obtains).(i.e. tensile sample exists value in a lateral direction
On the width of this band obtain) with in a longitudinal direction value possibility different, and generally than
These on longitudinal direction are high and low on elongation percentage in intensity.
In one embodiment, the carbon content of steel is 0.07～0.13%, and yield strength is
At least 960MPa.
In one embodiment, the carbon content of steel is 0.13～0.18%, and yield strength is
At least 1100MPa.
In one embodiment, wherein carbon content is at least 0.19%, preferably 0.23～0.30%
Between, and yield strength is at least 1300MPa.
The suitable ultimate tensile strength of the hot-rolled steel according to the present invention is 1700MPa.
According to second aspect, the present invention is embodied in for preparing hot-rolled high-strength microalloying
The method of steel band, this steel band has the thickness between 2～16mm, has the HAZ-of improvement
Soften the yield strength of repellence and at least 960MPa, have and comprise martensite, tempered martensite
And/or the microscopic structure of bainite, and wherein this steel contains in terms of weight %:
● 0.07～the C of 0.30%；
● 0.8～the Mn of 2.0%；
● 0.01～the Al of 0.08%sol；
● 0.2～the Cr of 1.5%；
● 0.1～the Mo of 0.7%；
● the B of 0.0005～0.005；
● 0.01～the Nb of 0.07%；
● the Si of most 0.5%；
● the P of most 0.03%；
● the S of most 0.015%；
● the Ti of most 0.05%；
● the V of most 0.1%；
● the Cu of most 0.2%；
● the Ni of most 0.2%；
● the N of most 0.008%；
● the calcium interpolation controlled for sulphide shape of the most most 0.015%；
● with other elements of the amount of impurity level, surplus is ferrum.
This band is higher than Ar3At a temperature of carry out hot finishing, wherein the method includes below at least
Step:
● finish rolling to 2～the final thickness of 16mm
● in most 10 seconds of last hot rolling pass, be enough to the microscopic structure through rolling
It is changed into the cooldown rate of the microscopic structure comprising martensite and/or bainite, cools down this hot-rolled strip
The coiling temperature of material to 20～500 DEG C.
This hot rolling technology is conventional hot rolling technology, whether from the thickness with 150～350mm
Slab (i.e. conventional continuous casting steel billet), or or (i.e. sheet blank continuous casting or very less than 150
To Strip casting) start.Preferably when steel is still for austenite, finish rolling has compact grained to provide
Steel, and good impact flexibility is thus provided.Preferably coiling temperature is low needing with realization
Engineering properties.Preferably coiling temperature is less than 400 DEG C.By rapid cooling after hot rolling or directly quench
Fire, the steel of preparation the type, it is thus achieved that excellent impact flexibility because occur from compact grained,
Processed austenite is to martensite and/or the phase transformation of bainite.It also improves surface quality,
Because removing initial iron scale before rolling in descaling mill.Also, it is not necessary to it is the most high
The additional annealing of expensive length processes to dissolve all of precipitate.In tropocal wood rolling line,
The warm rangeability of this slab to be rolled to 1100～1250 DEG C is reheated in reheating furnace, and
Keep several hours.In this case, the dissolving of particular carbon compound such as Cr and Mo carbide,
And the homogenization of tissue is the most thoroughly.On the other hand, under high heating-up temperature
The growth of austenite crystal does not make final products more crisp, because first passing through in the operation of rolling
The recrystallization during high temperature rolling in starting stage and the heat in the final stage of course of hot rolling
Turning of the deformed austenite crystal grain that the sluggishness that austenite during mechanical press changes causes and formed
Attenuate and changed austenite crystal.Cooling period on the run-out table, the austenite of gross distortion
Crystal grain is changed into the thinnest transmutation product.It is high that this causes being combined with excellent impact flexibility
Yield stress.If using sheet blank continuous casting and Direct Rolling facility (wherein in rolling beginning
Front element does not the most separate out as Cr and Mo carbide), then preparation cost and the production time
Also can reduce further.
According to the present invention, remain as austenite at steel, i.e. higher than Ar3Finishing temperature under should
Final hot rolled thickness made by steel.Band be cooled in last hot rolling pass after be not later than 10
Second starts, and the most quickly cools down it to allow austenite to be changed into bainite and/or martensite
Microscopic structure, cooldown rate is preferably at least 30 DEG C/s, be reduced to 20～500 DEG C batch temperature
Degree, is preferably decreased to the coiling temperature of 20～450 DEG C.The nearlyest shellfish completely of the result obtained
Family name's body and/or martensitic microstructure so that bainite and/or martensite content are preferably at least
90 volume %, preferably at least 95 volume %.This microscopic structure is not it is also preferred that contain and at high temperature formed
Ferrite and without pearlite composition, therefore make microscopic structure substantially completely for bainite/geneva
Body, the most for this purpose, ferrite side plate or acicular ferrite are considered as bainite
Tissue.In the coiling temperature scope less than 100 DEG C, not by martenaging martempering, although at this
Under a little low temperature, for low-carbon (LC) grade, may occur in which some self temperings, and when coiling temperature is at least
When 100 DEG C, martensite is tempered.At a temperature of higher than 200 DEG C, martensite is tempered and this carbon
It is precipitated.
In preferred embodiments, for containing most 0.12% the steel of carbon content, batch
Temperature is most 450 DEG C, more preferably 425 DEG C, the steel of the carbon content for containing at least 0.13%,
For most 275 DEG C, more preferably 250 or 225 DEG C.
In one embodiment, the acceleration cooling period after hot rolling and before batching, cold
But speed is 5～100 DEG C/s.
In one embodiment, final rolling temperature is higher than Ar3And also below 920 DEG C, and preferably
Also below 900 DEG C.
According to the 3rd aspect, automobile, truck, shipbuilding will be used for according to the steel of the present invention, execute
Work engineering, heave-load device, earth-moving equipment or the production of derrick car parts.
Following non-limiting example is utilized to further illustrate the present invention.Table 1 shows kind
The steel composition of each of S700, S960, S1100 and S1300.
In addition to the composition (except B and N(ppm) of table 1. steel, all in terms of weight % × 1000.All of steel
All through Ca process, imp=impurity level)
It is main by tempered martensite group that SEM microscopic structure shows that all of hot-rolled steel sample is respectively provided with
The microscopic structure become, the little carbide being characterised by Widmannstatten structure.Owing to these are relatively low
The high M of C steelsTemperature, and also due to be used for simulating the Slow cooling batching cooling, therefore will
Cause the tempering of martensite.Show several variants of orientation relationship between carbide and matrix
The pattern of carbide, be characterised by tempered martensite.Austenite grain boundary before is also visible
, and show that some along rolling direction extends, as used optics metallographic observation to arrive.By force
Degree level depends strongly on coiling temperature and (sees Fig. 1 and S1300 material of S1100 material
Fig. 2), its microscopic structure referred to required for being mainly made up of tempered martensite understands.
Fig. 3 shows that the steel (a, c) according to the present invention and comparative steel (b, d) are in Y-axis
On HAZ emollescence.Clearly visible, for the softening of the reduction of HAZ, the present invention's
Steel has exceeded comparative steel.Steel b and d respectively S960-Nb and S960+Cr-Nb(sees
Table 1), and a and c be respectively S960 base and S960+V.
Claims (11)
1. hot-rolled high-strength microalloy steel band, it has the thickness of 2～16mm, has and change
Kind HAZ-softens repellence, has and comprises martensite, tempered martensite and/or bainite
Microscopic structure, and wherein this steel contains in terms of weight %:
● 0.07～the C of 0.13%；
● 0.8～the Mn of 2.0%；
● 0.01～the Al of 0.08%sol；
● 0.2～the Cr of 1.5%；
● 0.1～the Mo of 0.7%；
● the B of 0.0005～0.005；
● 0.01～the Nb of 0.07%；
● the Si of most 0.5%；
● the P of most 0.03%；
● the S of most 0.015%；
● the Ti of most 0.05%；
● the V of most 0.1%；
● the Cu of most 0.2%；
● the Ni of most 0.2%；
● the N of most 0.008%；
● the calcium interpolation controlled for sulphide shape of the most most 0.015%；
● other elements of the amount of impurity level, surplus is ferrum；
The yield strength of this steel band is at least 960MPa.
2. hot-rolled high-strength microalloy steel band, it has the thickness of 2～16mm, has and change
Kind HAZ-softens repellence, has and comprises martensite, tempered martensite and/or bainite
Microscopic structure, and wherein this steel contains in terms of weight %:
● 0.13～the C of 0.18%；
● 0.8～the Mn of 2.0%；
● 0.01～the Al of 0.08%sol；
● 0.2～the Cr of 1.5%；
● 0.1～the Mo of 0.7%；
● the B of 0.0005～0.005；
● 0.01～the Nb of 0.07%；
● the Si of most 0.5%；
● the P of most 0.03%；
● the S of most 0.015%；
● the Ti of most 0.05%；
● the V of most 0.1%；
● the Cu of most 0.2%；
● the Ni of most 0.2%；
● the N of most 0.008%；
● the calcium interpolation controlled for sulphide shape of the most most 0.015%；
● other elements of the amount of impurity level, surplus is ferrum；
The yield strength of this steel band is at least 1100MPa.
Steel band the most according to claim 1, it has the content of niobium of at least 0.02%.
4., according to the steel band of claim 1 or 2, it has the nickel content being in impurity level.
5., according to the steel band of claim 1 or 2, it has the copper content being in impurity level.
6. the method preparing hot-rolled high-strength microalloy steel band, this steel band has 2～16
The thickness of mm, the HAZ-with improvement softens repellence, and the yield strength of at least 960MPa,
There is the microscopic structure comprising martensite, tempered martensite and/or bainite, and wherein this steel with
Weight % meter contains:
● 0.07～the C of 0.27%；
● 0.8～the Mn of 2.0%；
● 0.01～the Al of 0.08%sol；
● 0.2～the Cr of 1.5%；
● 0.1～the Mo of 0.7%；
● the B of 0.0005～0.005；
● 0.01～the Nb of 0.07%；
● the Si of most 0.5%；
● the P of most 0.03%；
● the S of most 0.015%；
● the Ti of most 0.05%；
● the V of most 0.1%；
● the Cu of most 0.2%；
● the Ni of most 0.2%；
● the N of most 0.008%；
● the calcium interpolation controlled for sulphide shape of the most most 0.015%；
● other elements of the amount of impurity level, surplus is ferrum；
Higher than Ar3At a temperature of by this band hot finishing, wherein the method at least comprises the following steps:
● finish rolling to 2～the final thickness of 16mm；
● after last hot rolling pass in most 10 seconds, be enough to roll microscopic structure
It is changed into the cooldown rate of the microscopic structure comprising martensite and/or bainite, hot-rolled band is cold
The coiling temperature of but to 20～500 DEG C.
Method the most according to claim 6, wherein coiling temperature is:
● for containing most 0.12% the steel of carbon content, most 450 DEG C, or
● the steel of the carbon content for containing at least 0.13%, most 275 DEG C.
8. according to the method for claim 6 or 7, adding the most after hot rolling and before batching
The cooldown rate of the cooling period of speed is 5～100 DEG C/s.
9., according to the method for claim 6 or 7, wherein final rolling temperature is higher than Ar3And also below
920℃。
Method the most according to claim 9, wherein final rolling temperature is less than 900 DEG C.
11. according to the steel band of Claims 1 to 5 automobile, heave-load device, earth-moving equipment or
Purposes in the production of the parts of derrick car.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| EP11173383 | 2011-07-10 | ||
| EP11173383.8 | 2011-07-10 | ||
| PCT/EP2012/063515 WO2013007729A1 (en) | 2011-07-10 | 2012-07-10 | Hot-rolled high-strength steel strip with improved haz-softening resistance and method of producing said steel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN103649355A CN103649355A (en) | 2014-03-19 |
| CN103649355B true CN103649355B (en) | 2016-08-17 |
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ID=46508348
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| CN201280034223.9A Expired - Fee Related CN103649355B (en) | 2011-07-10 | 2012-07-10 | Have the HAZ-of improvement soften repellence hot-rolled high-strength steel band and the method that produces described steel |
Country Status (3)
| Country | Link |
|---|---|
| EP (1) | EP2729590B1 (en) |
| CN (1) | CN103649355B (en) |
| WO (1) | WO2013007729A1 (en) |
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| EP2325435B2 (en) | 2009-11-24 | 2020-09-30 | Tenaris Connections B.V. | Threaded joint sealed to [ultra high] internal and external pressures |
| US9163296B2 (en) | 2011-01-25 | 2015-10-20 | Tenaris Coiled Tubes, Llc | Coiled tube with varying mechanical properties for superior performance and methods to produce the same by a continuous heat treatment |
| IT1403689B1 (en) | 2011-02-07 | 2013-10-31 | Dalmine Spa | HIGH-RESISTANCE STEEL TUBES WITH EXCELLENT LOW TEMPERATURE HARDNESS AND RESISTANCE TO CORROSION UNDER VOLTAGE SENSORS. |
| GB2525337B (en) | 2013-01-11 | 2016-06-22 | Tenaris Connections Ltd | Galling resistant drill pipe tool joint and corresponding drill pipe |
| US9803256B2 (en) | 2013-03-14 | 2017-10-31 | Tenaris Coiled Tubes, Llc | High performance material for coiled tubing applications and the method of producing the same |
| EP2789700A1 (en) | 2013-04-08 | 2014-10-15 | DALMINE S.p.A. | Heavy wall quenched and tempered seamless steel pipes and related method for manufacturing said steel pipes |
| EP2789701A1 (en) | 2013-04-08 | 2014-10-15 | DALMINE S.p.A. | High strength medium wall quenched and tempered seamless steel pipes and related method for manufacturing said steel pipes |
| WO2014185405A1 (en) | 2013-05-14 | 2014-11-20 | 新日鐵住金株式会社 | Hot-rolled steel sheet and production method therefor |
| WO2014207656A1 (en) | 2013-06-25 | 2014-12-31 | Tenaris Connections Ltd. | High-chromium heat-resistant steel |
| US10837079B2 (en) | 2014-01-24 | 2020-11-17 | Rautaruukki Oyj | Hot-rolled ultrahigh strength steel strip product |
| WO2016000444A1 (en) * | 2014-06-30 | 2016-01-07 | 宝山钢铁股份有限公司 | Ultra-high-strength and ultra-high-toughness oil casing and manufacturing method thereof |
| DE102014017273A1 (en) * | 2014-11-18 | 2016-05-19 | Salzgitter Flachstahl Gmbh | High strength air hardening multiphase steel with excellent processing properties and method of making a strip of this steel |
| DE102015111177A1 (en) * | 2015-07-10 | 2017-01-12 | Salzgitter Flachstahl Gmbh | High strength multi-phase steel and method of making a cold rolled steel strip therefrom |
| US11124852B2 (en) | 2016-08-12 | 2021-09-21 | Tenaris Coiled Tubes, Llc | Method and system for manufacturing coiled tubing |
| US10434554B2 (en) | 2017-01-17 | 2019-10-08 | Forum Us, Inc. | Method of manufacturing a coiled tubing string |
| CN108486494B (en) * | 2018-06-05 | 2019-06-21 | 西北工业大学 | The production method of vanadium micro-alloying 1300MPa grade high-strength hot rolled steel plate and cold-rolled biphase steel plate |
| CN109680211A (en) * | 2018-12-28 | 2019-04-26 | 首钢集团有限公司 | A kind of manufacturing method of vehicle structure steel and its manufacturing method and automobile structure |
| WO2020169410A1 (en) * | 2019-02-18 | 2020-08-27 | Tata Steel Ijmuiden B.V. | High strength steel with improved mechanical properties |
| EP3744862A1 (en) | 2019-05-29 | 2020-12-02 | ThyssenKrupp Steel Europe AG | Hot rolled flat steel product with optimised welding properties and method for producing such a flat steel product |
| EP3926064B1 (en) * | 2020-06-16 | 2022-08-24 | SSAB Technology AB | High strength strip steel product and method of manufacturing the same |
| CN113106336B (en) * | 2021-03-17 | 2022-06-10 | 唐山钢铁集团有限责任公司 | Ultrahigh-strength dual-phase steel capable of reducing softening degree of laser welding head and production method thereof |
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| CN103649355A (en) | 2014-03-19 |
| EP2729590B1 (en) | 2015-10-28 |
| WO2013007729A1 (en) | 2013-01-17 |
| EP2729590A1 (en) | 2014-05-14 |
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