CN1609257A - Acicular constituent high strength weathering resistant steel and producing method thereof - Google Patents
Acicular constituent high strength weathering resistant steel and producing method thereof Download PDFInfo
- Publication number
- CN1609257A CN1609257A CN 200410061112 CN200410061112A CN1609257A CN 1609257 A CN1609257 A CN 1609257A CN 200410061112 CN200410061112 CN 200410061112 CN 200410061112 A CN200410061112 A CN 200410061112A CN 1609257 A CN1609257 A CN 1609257A
- Authority
- CN
- China
- Prior art keywords
- steel
- present
- high strength
- low
- weather resistance
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
The present invention relates to high strength high weather resistance steel with needle structure and its production process, and belongs to the field of low alloy steel making. The present invention adopts very low carbon content to result in normal temperature dissolvability in alpha-Fe not higher than 0.0218 wt%, adds Cu, Cr, Ni, Mo, Nb, Ti, Al, Zr, RE and Ca, and ensures the main structure is needle-like structure for excellent weather resistance. The steel of the present invention is produced by means of hot rolling technology and relaxation-separation control technology and has low production cost and short production period. It has excellent weather resistance, excellent toughness, and excellent weldability needing no preheating before welding and heat treatment after welding, and may be used widely in bridge, building, traffic facility, sea platform, etc.
Description
Technical field
The present invention relates to a kind of acicular structure high strength weathering steel and production method thereof, the non-quenched acicular structure high strength weathering steel and the production method thereof of specifically a kind of low-temperature flexibility and welding property excellence belong to low alloy steel and make the field.
Background technology
Before the present invention, HPS 70W steel among the standard A STMA709/A709M-01b of American Society Testing and Materials of close intensity rank is arranged, its carbon content is less than or equal to 0.11%, generally about 0.09%, the welding cold crack sensitivity coefficient is higher, therefore need complicated weldprocedure, need take modified thermal treatment to Plate Steel simultaneously.This steel also contains 0.04%～0.08% vanadium, in the postwelding process of cooling, can separate out the carboritride of vanadium, influences the welding toughness of steel.Also just like calendar year 2001 United States Navy Department Focht; " ULCB weathering steel " patent of Eric M invention, patent No. US6315946, its on 2 inch thickness yield strength greater than 455MPa.What this steel adopted is hot mechanical controlled rolling technology, does not need modified or temper.This steel C 0.015%～0.035%, although also accomplish the level of utmost point low-carbon (LC), weak point is regulation molybdenum content≤0.50% in its composition design, copper content 0.20%～0.40%, chromium content 0.40%～0.70%, vanadium≤0.10%.Increase its hardening capacity for proof strength also need add 0.0015%～0.0035% boron simultaneously, promote or finish bainite transformation.Therefore the higher welding property that causes of alloy content reduces.And boron belongs to light element, forms carbide and nitride easily, and is poly-partially at original austenite crystal prevention, forms the flexible boron phase that reduces steel.High v element adds welding property and the low-temperature flexibility that has also reduced steel.On its production technique, this steel promptly directly quickens cooling after overheated mechanical controlled rolling technology, does not make full use of that niobium etc. is separated out and dislocation is mutual strengthens and the structure refinement effect.
Summary of the invention
The non-quenched acicular structure high strength weathering steel and the production method thereof that the purpose of this invention is to provide a kind of low-temperature flexibility and welding property excellence, the composition simplicity of design of steel, do not add the hardening capacity element boron, a kind of work simplification is provided simultaneously, needn't heat-treat, can reduce cost, shorten the production method of production cycle, make the steel plate of output integrate good weathering resistance and excellent low-temperature flexibility and weldability, even still do not need preheating before the steel plate that 50mm is thick welds, postwelding does not need thermal treatment.
The present invention in order to achieve the above object, designed the non-modified acicular structure high strength weathering steel of a kind of low-temperature flexibility and welding property excellence, the chemical ingredients that it is characterized in that steel percentage is by weight counted: C0.01～0.04, Si 0.15～0.30, Mn 1.30～1.60, P≤0.060, S≤0.010, Cu 0.15～0.50, Cr 0.20～0.40, Ni 0.10～0.24, Mo 0.10～0.30, Nb 0.030～0.060 and Ti≤0.030, Als≤0.035, in Zr≤0.010 and RE≤0.40kg/t steel or Ca≤0.0050 two or more, surplus is Fe and inevitably is mingled with, must satisfy welding cold crack sensitivity coefficient: Pcm=C+Si/30+ (Mn+Cu+Cr)/20+Mo/15+Ni/60+V/10+5B≤0.18% in addition.
The reason of C, Si, Mn, P, S, Cu, Cr, Ni, Mo, Nb, Ti, Als, Zr, RE and Ca limited amount among the present invention below is described in detail in detail.
C content of the present invention is chosen in 0.01%～0.04%.C generally serves as the reinforcement constituent element in ferrous materials, if dissolve in the matrix, can play the effect of solution strengthening, increases carbon content and can promote to form carbide and martensite.In order to improve weldability, low-temperature flexibility and weather resistance, carbon content of the present invention is extremely low, promptly near or less than the maxima solubility 0.0218% of carbon in ferrite at normal temperatures.In the transition process of γ → α, owing to separating out of Nb (CN), the solubility limit of carbon is not easy to be exceeded in the ferrite, thereby forms εTan Huawu or Fe in microstructure
3The possibility of C is minimum, and the occurrence probability of high-carbon M-A-C constituent element is also very little, and the inhomogeneous distribution of promptly less generation C atom has guaranteed the even of structure of steel.Electropotential more reaches unanimity between each microcell, has improved the weather resistance of steel.And when reducing carbon content, higher content of niobium is added in permission in steel, contain the higher steel grade of niobium, austenite just can be processed in higher rolling temperature, like this can be by postponing austenite to ferritic transformation, improve the volume fraction of acicular structure and NbC and separate out and obtain additional strengthening effect.Carbon content can not unconfinedly reduce, carbon content should be able to be in that guarantee can be owing to the acicular structure phase transformation not exclusively forms under the martensitic prerequisite, be enough to again react and form NbC with microalloy element Nb, therefore carbon content should not be lower than 0.01%, otherwise, can not form enough NbC with proof strength.Carbon content has then increased the reorganization of C atom in the phase transformation of γ → α as greater than 0.04%, and the carbide of generation is owing to forming the corrosion resisting property that effective negative electrode reduces steel, and welding property and low-temperature performance also decrease.
Si content of the present invention is 0.15%～0.30%, and Si mainly improves the intensity of steel with the solution strengthening form, also be simultaneously the deoxidant element in the steel, but content can not be too high, in order to avoid reduce the toughness and the welding property of steel.
Mn content of the present invention is chosen in 1.30%～1.60%.Mn is important highly malleablized element, it is austenite stabilizer element, can enlarge the austenitic area in the iron-carbon diagram, promote the middle temperature structural transformation of steel, obtain the microtexture based on acicular structure, this tissue is compared with traditional ferrite pearlific steel, has the better tissues homogeneity, good weather resistance, high intensity and excellent low-temperature flexibility.Contain 1% Mn and can improve tensile strength 100MPa approximately.Along with the increase of manganese content, the intensity of steel obviously increases, but impact transition temperature (ITT) changes hardly.But too high Mn impairs the toughness of steel, and for the performance that obtains steel of the present invention, also is warm structural transformation during unnecessary, too low Mn then can not effectively promote.
P of the present invention≤0.060%, high P content can increase substantially the weathering resistance of steel, and can rationally gather partially by an amount of of P, remedies the deficiency that ultra-low carbon steel intergranular intensity reduces.Its sufficient quantity is≤0.060%.
S of the present invention≤0.010%, high S content not only can make steel plate produce notable difference to performance in length and breadth, also reduce the low-temperature flexibility of steel and Z simultaneously to performance.Sulfide inclusion can make the weather resistance of steel also obviously reduce.Its sufficient quantity is≤0.010%.
Cu can improve the hardening capacity of steel, mainly plays solid solution and precipitation strength effect in steel, also can improve the weather resistance of steel by the suitable proportion of Cu-Cr-Ni simultaneously, helps obtaining good low-temperature flexibility in addition, increases the antifatigue crack propagation ability of steel.Cu. content is less than 0.15%, and its precipitation strength effect is not obvious.The add-on of Cu was greater than 0.50% o'clock in the present invention, and the steel plate welding heat influence area toughness can reduce, and easily produced check crack in steel billet heat-processed.Its sufficient quantity is 0.15%～0.50%.
Cr also is the effective element that improves hardening capacity, and a certain amount of Cr can make steel obtain good weather resistance.Under the situation of the compound interpolation of Cu-Cr-Ni, Cr helps to improve hardening capacity and weather resistance, and its sufficient quantity is 0.20%～0.40%.
Ni can improve hardening capacity, has certain strengthening effect, and the Ni of adding 1% can improve the about 20MPa of steel strength.When improving intensity, Ni can also improve the low-temperature flexibility of steel significantly.Base material and welded heat affecting zone low-temperature flexibility are increased substantially.Ni can also effectively stop the hot-short check crack that causes of Cu.Ni can significantly improve the weather resistance of steel, especially sea water corrosion resistant.Its add-on is less than 0.10%, and then Ni does not have effect, but too high levels easily causes the steel plate iron scale to be difficult to come off and increases the cost of steel.The sufficient quantity of Ni is 0.10%～0.24% among the present invention.
The content of Mo is 0.10%～0.30%.Mo can increase hardening capacity, improves the intensity of steel.When Mo, Nb is more effective for stoping austenite recrystallization, and to change the beginning temperature be effective elements to Mo reducing acicular structure, can make steel obtain acicular structure tissue more completely in the speed of cooling scope of broad.When Mo increased, along with acicular structure changes the remarkable decline that begins temperature, the intensity of steel obviously improved.But too high Mo can make the low-temperature flexibility of steel significantly worsen.Excessive Mo also can form martensite when welding, cause the brittle increase of welding joint.So the suitable upper limit is controlled to be 0.30%.
Nb is strong carboritride forming element, can improve the austenite recrystallization temperature of steel.Austenite can be rolled under higher rolling temperature, and by postponing austenite to ferritic transformation, improves the acicular structure volume fraction.The precipitation strength effect of Nb in the controlled rolling continuous cooling process in addition, the strain inducing of the carbonitride by Nb are separated out can the pinning austenite crystal, and refine austenite crystal grain also improves intensity and low-temperature flexibility.Nb sometimes separately or with the compound adding of Ti to improve the mechanical property of steel by precipitation strength.But too high Nb is also easy and elements such as Fe, C form the low melting point eutectic things, thereby increases the tendency that weld metal produces thermal crack.The sufficient quantity of Nb is 0.030%～0.060% among the present invention.
Also contain among Ti, Als, Zr and RE or the Ca two or more in the steel of the present invention.
Therefore Ti is strong nitride forming element, and the nitride of Ti is the pinning austenite grain boundary effectively, helps to control growing up of austenite crystal, the suitable content of Ti is controlled at≤and 0.030%.
Steel Als content of the present invention is controlled at≤and 0.035%, Al is the main deoxidant element in the steel.Al content will cause the oxide inclusion of Al to increase greater than 0.035%, reduce the purity of steel, be unfavorable for the toughness and the weather resistance of steel.The fusing point of Al is higher, and aborning, Al can be used for stoping grain growth.
Zr among the present invention≤0.010%, the oxide compound that an amount of Zr forms in pyroprocess can be used as acicular structure forming core particle, forms a large amount of acicular structures at welded heat affecting zone, to improve steel plate Chinese People's Anti-Japanese Military and Political College heat input welding property.
Steel of the present invention carries out rare earth or calcium aborning to be handled, and it mainly acts on all is for making the sulfide inclusion nodularization, to improve in length and breadth to performance difference, improving Z to performance.And the electrode potential difference by reducing sulfide and matrix on every side is to improve corrosion resistance; When carrying out the rare earth processing, form one deck rare earth protective membrane on the steel plate top layer, improve the weather resistance of steel.But too high RE adds in the steel, forms oarse-grained rare earth oxide easily and is mingled with, and influences the over-all properties of steel, and the add-on of RE is≤the 0.40kg/t steel among the present invention; Ca≤0.0050% in the steel when carrying out the calcium processing.
The invention belongs to low alloy steel and make the field, the present invention is except that containing above-mentioned chemical ingredients, surplus is Fe and inevitably is mingled with, also must satisfy welding cold crack sensitivity coefficient: Pcm=C+Si/30+ (Mn+Cu+Cr)/20+Mo/15+Ni/60+V/10+5B≤0.18% simultaneously.
The present invention also provides the production method of above-mentioned acicular structure high strength weathering steel, adopt molten iron pre-desulfurization, the converter top bottom blowing, RH vacuum circulation degassing technology, carrying out rare earth or calcium simultaneously handles, whole process protection cast, the chemical ingredients that it is characterized in that steel percentage is by weight counted: C 0.01～0.04, Si 0.15～0.30, Mn 1.30～1.60, P≤0.060, S≤0.010, Cu 0.15～0.50, Cr 0.20～0.40, Ni 0.10～0.24, Mo 0.10～0.30, Nb 0.030～0.060 and Ti≤0.030, Als≤0.035, Zr≤0.010 and add in RE≤0.40kg/t steel or Ca≤0.0050 two or more, surplus is Fe and inevitably is mingled with; With steel billet behind 1250 ℃ of austenitizings, adopt two stage rolling, breaking down start rolling temperature 〉=1150 ℃, accumulative total draft 〉=60%, finish rolling start rolling temperature≤950 ℃, finish rolling end temp≤820 ℃, three roads, end accumulative total draft 〉=40%, rolled back steel plate relaxation time 20～100 seconds, the rate of cooling with 5～10 ℃/S is cooled to 400～700 ℃ then, and air cooling is to room temperature again.
The hot mechanical controlled rolling technology+relaxation of the rolling employing of steel billet among the present invention-separate out control techniques.Steel billet is at 1250 ℃ of abundant austenitizings, make the abundant solid solution of microalloy element, breaking down start rolling temperature 〉=1150 ℃, breaking down is carried out in the austenite recrystallization district, owing to added higher content of niobium in the steel of the present invention, significantly improved the recrystallization temperature of steel, be convenient to realize that austenite recrystallization district high temperature depresses rolling greatly, can realize accumulative total draft 〉=60%, obtain the austenite crystal of enough refinements; Steel begins to enter the non-recrystallization district at 950 ℃ and begins finish rolling, require start rolling temperature≤950 ℃, finish rolling end temp≤820 ℃, last three roads accumulative total draft 〉=40% is separated out so that produce the carbon nitrogen of the niobium etc. of a large amount of distortion dislocation, deformed belt and various size of tangling in the deformation austenite; In rolling 20～100 seconds the relaxation time in back, because rearranging of high density dislocation produces cell structure, by completeization of cell wall, processes such as intercellular misorientation increasing form substructure, make and organize refinement more.Meanwhile, the carbon nitrogen precipitate pinning substructure of niobium makes its stabilization; Subsequently by 5～10 ℃/S acceleration cooling, promote the refinement of organizing after the phase transformation; Be cooled to 400～700 ℃, warm structural transformation in fully carrying out, air cooling is to room temperature again.
Acicular structure high strength weathering steel of the present invention and production method thereof have following advantage:
1. composition of steel simplicity of design of the present invention, the composition of steel are designed to utmost point low-carbon (LC) Cu-Cr-Ni-Mo composition series, add the high P of high Nb, do not add the hardening capacity element boron.The master control that obtains steel is organized as acicular ferrite (greater than 60%), and more even than general super carbon bainite structure of steel, the microcell difference in Electrode Potential is littler between tissue, and the weather resistance of steel is better, and low-temperature flexibility is excellent more.
2. steel of the present invention adds higher P element can significantly improve weather resistance.Add higher Nb element and can improve austenite recrystallization temperature, realize the controlled rolling of high temperature heavy reduction.Relaxation after the finish rolling-separate out CONTROL PROCESS to have guaranteed that Nb (CN) fully separates out.Dynamically separate out and relaxation is separated out the second phase particle pinning effect of deformation dislocation and phase transformation dislocation has been guaranteed high strength and high tenacity.
3. steel use heat of the present invention machinery controlled rolling+relaxation-separate out control techniques to produce need not be modified or heat treatment step such as tempering, shortened the production cycle, reduced production cost.And overcome the deficiency of steel plate specification heat-treated stove restriction.
4. the steel of the present invention's production has splendid obdurability coupling, excellent low-temperature flexibility has excellent welding property simultaneously, can simplify weldprocedure, improve welding efficiency, steel of the present invention can be widely used in engineering structures such as bridge, building, traffic, ocean platform.
Embodiment
Embodiment 1: according to composition of steel requirement of the present invention, smelt steel of the present invention on 80 tons of oxygen top and bottom combined blown converters, after the RH vacuum outgas is handled, carry out rare earth and handle, adopt the continuous casting of whole process protectiveness; The main chemical compositions of heat analysis steel sees Table " invention steel 1 " in 1; Steel billet is come out of the stove rolling behind 1250 ℃ of austenitizings, and start rolling temperature is 1180 ℃, and the accumulative total draft is 70%, 67%, 60%; The finish rolling start rolling temperature is respectively 915 ℃, 935 ℃, 947 ℃, and the finish rolling end temp is respectively 773 ℃, 806 ℃, 812 ℃, last three roads accumulative total draft 45%; Rolling the back relaxation time is 20 seconds, is cooled to 580 ℃ with 6 ℃/S, 8 ℃/S, the rate of cooling of 10 ℃/S respectively behind the relaxation, and the air cooling steel plate is to room temperature then.The steel plate thickness difference 32,50, the 60mm that produce.
The chemical ingredients of the comparative steel 2 of steel of the present invention and HPS 70W comparative steel 1, US6315946 patent, mechanical property, welding property and corrosion resistance contrast see table 1～3 for details.
Comparative steel 2 unexposed its tensile strength of US6315946 patent in the table 1, but on 2 inch thickness yield strength greater than 455MPa; Corrosion resistance index I calculation formula is the Legault-Leckie formula of revising among the standard A STM G101-01 of American Society Testing and Materials " Standard Guide for Estimating the AtmosphericCorrosion Resistance of Low-Alloy Steels " in the table, its value is high more, and the expression corrosion resistance is strong more; Calculation formula I=26.01 (%Cu)+3.88 (%Ni)+1.20 (%Cr)+1.49 (%Si)+17.28 (%P)-7.29 (%Cu) is (%Ni) (%P)-33.39 (%Cu) (%Ni)-9.10
2
Table 1
| Invention steel 1 | Invention steel 2 | Comparative steel 1 | Comparative steel 2 | |||
| Divide | ??????C | ????0.03 | ????0.02 | ????≤0.11 | ????0.02 | |
| ??????Si | ????0.21 | ????0.25 | ????0.30～0.50 | ????0.25 | ||
| ??????Mn | ????1.34 | ????1.49 | ????1.10～1.35 | ????1.85 | ||
| ??????P | ????0.008 | ????0.045 | ????≤0.020 | ????0.012 | ||
| ??????S | ????0.006 | ????0.008 | ????≤0.006 | ????0.004 | ||
| ??????Cu | ????0.29 | ????0.40 | ????0.25～0.40 | ????0.36 | ||
| ??????Cr | ????0.38 | ????0.25 | ????0.45～0.70 | ????0.55 | ||
| ??????Ni | ????0.24 | ????0.19 | ????0.25～0.40 | ????0.30 | ||
| ??????Mo | ????0.25 | ????0.15 | ????0.02～0.08 | ????-- | ||
| ??????V | Remaining | ????-- | ????0.04～0.08 | ????-- | ||
| ??????Nb | ????0.035 | ????0.055 | Remaining | ????0.050 | ||
| ??????Ti | Remaining | ????0.017 | Remaining | ????0.025 | ||
| ??????B | Remaining | Remaining | Remaining | ????0.0030 | ||
| ??????Zr | Remaining | ????0.008 | Remaining | ????-- | ||
| ??????N | Remaining | Remaining | ????≤0.015 | ????0.008 | ||
| ??????Als | ????0.020 | ????0.035 | ????0.010～0.040 | ????0.025 | ||
| RE (add-on) | 0.15kg/t steel | ????0 | ????0 | ????0 | ||
| ??????Ca | Remaining | ????0.0030 | In right amount | ????-- | ||
| Yield strength (MPa) | ????????????490～540 | ????≥485 | ????≥455 | |||
| Tensile strength (MPa) | ????????????590～650 | ????586～760 | ????-- | |||
| Summer is than V-type ballistic work (J) | -23℃ | ????????????-- | ????210～298 | ????-- | ||
| -34℃ | ????????????-- | ????≥48 | ????≥41 | |||
| -40℃ | ????????????210～298 | ????-- | ????-- | |||
| Welding cold crack sensitivity indices P cm | ????0.16 | ????0.16 | About 0.22 | ????0.19 | ||
| Corrosion resistance index I | ????6.0 | ????6.1 | About 6.7 | ????6.6 | ||
By table 1 as seen, the erosion resistance index of steel of the present invention and comparative steel is close, shows that its weathering resistance is in same level.Steel welding cold crack sensitivity index of the present invention is starkly lower than comparative steel, shows that its weldability is excellent more.
Embodiment 2: according to composition of steel requirement of the present invention, smelt steel of the present invention on 80 tons of oxygen top and bottom combined blown converters, after the RH vacuum outgas is handled, adopt the calcium treatment technology, the continuous casting of whole process protectiveness; Chemical ingredients sees Table 1 " invention steel 2 "; Steel billet is come out of the stove behind 1250 ℃ of austenitizings, and the breaking down start rolling temperature is 1200 ℃, and the accumulative total draft is 70%, 63%; The finish rolling start rolling temperature is respectively 945 ℃, 915 ℃, and the finish rolling end temp is respectively 784 ℃, 805 ℃, last three roads accumulative total draft 48%, 41%; Roll the back relaxation time be 35 seconds, 100 seconds, behind the relaxation respectively the rate of cooling with 5 ℃/S, 9 ℃/S be cooled to 650 ℃, 680 ℃, air cooling is to room temperature.The steel plate of rolling thickness difference 25.5,51mm.
The steel that embodiment 1, embodiment 2 produces carries out mechanical properties test, the results are shown in Table 2 and table 3.
Table 2 invention steel 1 mechanical property
| Thickness of slab (mm) | Tensile property (laterally) | -40 ℃ of impact of collision merits | ||
| ??R eL(MPa) | ?Rm(MPa) | ??A(％) | ??(A KV/J) | |
| 32 | ??530??520 | ?620??615 | ??21.0??19.0 | ??251??295??219 |
| 50 | ??520??540 | ?600??610 | ??23.5??18.5 | ??263??214??279 |
| 60 | ??515??495 | ?590??595 | ??20.0??22.5 | ??279??280??298 |
Table 3 invention steel 2 mechanical propertys
| Thickness of slab (mm) | Tensile property (laterally) | -40 ℃ of impact of collision merits | ||
| ????R eL(MPa) | ??Rm(MPa) | ??A(％) | ????(A KV/J) | |
| ??25.5 | ????530??540 | ??650??645 | ??20.0??24.0 | ????210??216??217 |
| ??51 | ????500??490 | ??610??600 | ??23.5??23.5 | ????243??217??298 |
By table 2 and table 3 as seen, steel of the present invention has excellent low-temperature flexibility, and-40 ℃ of impact of collision merits are all more than 210J.Low-temperature flexibility is all far above comparative steel.
Steel of the present invention can be widely used in welded constructions such as bridge, building, traffic, boats and ships, offshore production platform, has extremely wide application prospect.
Claims (2)
1 one kinds of acicular structure high strength weathering steels, the chemical ingredients that it is characterized in that steel percentage is by weight counted: C0.01～0.04, Si0.15～0.30, Mn1.30～1.60, P≤0.060, S≤0.010, Cu0.15～0.50, Cr0.20～0.40, Ni0.10～0.24, Mo0.10～0.30, Nb0.030～0.060 and Ti≤0.030, Als≤0.035, Zr≤0.010 and add in RE≤0.40kg/t steel or Ca≤0.0050 two or more, surplus is Fe and inevitably is mingled with, must satisfy welding cold crack sensitivity coefficient: Pcm=C+Si/30+ (Mn+Cu+Cr)/20+Mo/15+Ni/60+V/10+5B≤0.18% in addition.
2 one kinds of production methods of producing the acicular structure high strength weathering steel of claim 1, adopt molten iron pre-desulfurization, the converter top bottom blowing, RH vacuum circulation degassing technology, carrying out rare earth or calcium simultaneously handles, whole process protection cast, the chemical ingredients that it is characterized in that steel percentage is by weight counted: C0.01～0.04, Si0.15～0.30, Mn1.30～1.60, P≤0.060, S≤0.010, Cu0.15～0.50, Cr0.20～0.40, Ni0.10～0.24, Mo0.10～0.30, Nb0.030～0.060 and Ti≤0.030, Als≤0.035, Zr≤0.010 and add in RE≤0.40kg/t steel or Ca≤0.0050 two or more, surplus is Fe and inevitably is mingled with; With steel billet behind 1250 ℃ of abundant austenitizings, adopt two stage rolling, breaking down start rolling temperature 〉=1150 ℃, finish rolling start rolling temperature≤950 ℃, finish rolling end temp≤820 ℃, last three roads accumulative total draft 〉=40% rolled back steel plate relaxation time 20～100 seconds, rate of cooling with 5～10 ℃/S is cooled to 400～700 ℃ then, and air cooling is to room temperature again.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2004100611124A CN1323187C (en) | 2004-11-16 | 2004-11-16 | Acicular constituent high strength weathering resistant steel and producing method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2004100611124A CN1323187C (en) | 2004-11-16 | 2004-11-16 | Acicular constituent high strength weathering resistant steel and producing method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1609257A true CN1609257A (en) | 2005-04-27 |
| CN1323187C CN1323187C (en) | 2007-06-27 |
Family
ID=34764428
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB2004100611124A Expired - Fee Related CN1323187C (en) | 2004-11-16 | 2004-11-16 | Acicular constituent high strength weathering resistant steel and producing method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN1323187C (en) |
Cited By (25)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100345640C (en) * | 2005-08-31 | 2007-10-31 | 广州珠江钢铁有限责任公司 | Technology of producing Ti micro alloyed high weather resistant steel plate using thin plate blank continuous casting continuous milling process |
| CN100419115C (en) * | 2006-11-23 | 2008-09-17 | 武汉钢铁(集团)公司 | Ultrahigh-strength atmospheric-corrosion resistant steel |
| CN100435987C (en) * | 2006-11-10 | 2008-11-26 | 广州珠江钢铁有限责任公司 | Method for manufacturing 700MPa high-strength weathering steel based on thin slab continuous casting and rolling flow by use of Ti microalloying process |
| CN100455692C (en) * | 2006-12-08 | 2009-01-28 | 武汉钢铁(集团)公司 | High-strength weathering steel and method of manufacturing same |
| CN100460550C (en) * | 2006-08-22 | 2009-02-11 | 武汉钢铁(集团)公司 | Sea water corrosion resistant steel for ocean drilling/production platform and preparation method thereof |
| CN101792888A (en) * | 2010-03-17 | 2010-08-04 | 首钢总公司 | High-strength weathering steel and method for producing same |
| CN101376953B (en) * | 2007-08-28 | 2010-08-11 | 宝山钢铁股份有限公司 | High-corrosion resistant high-strength weather resisting steel and manufacturing method thereof |
| CN101875994A (en) * | 2010-03-31 | 2010-11-03 | 湖北猴王焊材有限公司 | Novel weathering resistant steel microalloying compound core-spun yarn |
| CN101892431A (en) * | 2010-07-07 | 2010-11-24 | 江苏省沙钢钢铁研究院有限公司 | Hot rolled weatherproof bridge steel with yield strength of 500 MPa level and manufacturing method thereof |
| CN101476080B (en) * | 2008-12-26 | 2011-01-26 | 首钢总公司 | Low welding crack sensitivity, quenching and tempering, high rigid plate and manufacturing method thereof |
| CN102392196A (en) * | 2011-11-15 | 2012-03-28 | 内蒙古包钢钢联股份有限公司 | High-strength high-tenacity rare earth-containing steel material for Z-type steels |
| CN101649413B (en) * | 2008-08-15 | 2012-03-28 | 宝山钢铁股份有限公司 | Ultra-strength and high toughness maraging steel and manufacturing method thereof |
| CN102397884A (en) * | 2010-09-16 | 2012-04-04 | 鞍钢股份有限公司 | Method for controlling crazing defect of surface of strip steel in high-Cu steel grade |
| CN102605287A (en) * | 2012-03-09 | 2012-07-25 | 武汉钢铁(集团)公司 | Steel for high-ductility anti-seismic structure with yield ratio smaller than or equal to 0.70 and production method of steel |
| CN101928894B (en) * | 2009-06-25 | 2012-09-19 | 宝山钢铁股份有限公司 | High-strength weather resisting steel with Cu2-xS dispersed precipitates and manufacturing method thereof |
| CN103194695A (en) * | 2013-04-07 | 2013-07-10 | 武汉钢铁(集团)公司 | Steel with stable oxide layer for pretreatment-free high-strength container and manufacture method of steel |
| CN103736945A (en) * | 2013-12-05 | 2014-04-23 | 天水星火机床有限责任公司 | Method for reducing molten iron casting cracks |
| CN105063509A (en) * | 2015-07-27 | 2015-11-18 | 武汉钢铁(集团)公司 | Structural steel with yield strength of 500 MPa for bridges and production method of structural steel |
| CN106222559A (en) * | 2016-08-30 | 2016-12-14 | 南阳汉冶特钢有限公司 | A kind of Novel ocean platform steel steel plate and production method thereof |
| CN107365940A (en) * | 2017-08-16 | 2017-11-21 | 北京科技大学 | A kind of preparation method and application of 700MPa levels Ultra-fine Grained high-strength weathering steel |
| CN109112392A (en) * | 2018-07-17 | 2019-01-01 | 张家港宏昌钢板有限公司 | The high tough high fatigue property Weather-resistance bridge steel plate of TMCP type and preparation method |
| CN109252092A (en) * | 2018-09-30 | 2019-01-22 | 燕山大学 | It is a kind of to exempt from coating weathering steel and preparation method thereof containing rare earth element |
| WO2020237976A1 (en) * | 2019-05-28 | 2020-12-03 | 南京钢铁股份有限公司 | Superfine acicularly-structured structural steel and production method therefor |
| CN112080702A (en) * | 2020-09-16 | 2020-12-15 | 燕山大学 | Weather-resistant bridge steel with impact absorption power of not less than 60J at-60 ℃ in welded coarse grain heat affected zone |
| CN114959451A (en) * | 2022-04-25 | 2022-08-30 | 中国科学院金属研究所 | Weather-resistant and fire-resistant structural steel for south-sea marine environment |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1132958C (en) * | 2001-10-17 | 2003-12-31 | 武汉钢铁(集团)公司 | High-performance refractory weather-resisting building steel and its production method |
-
2004
- 2004-11-16 CN CNB2004100611124A patent/CN1323187C/en not_active Expired - Fee Related
Cited By (30)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100345640C (en) * | 2005-08-31 | 2007-10-31 | 广州珠江钢铁有限责任公司 | Technology of producing Ti micro alloyed high weather resistant steel plate using thin plate blank continuous casting continuous milling process |
| CN100460550C (en) * | 2006-08-22 | 2009-02-11 | 武汉钢铁(集团)公司 | Sea water corrosion resistant steel for ocean drilling/production platform and preparation method thereof |
| CN100435987C (en) * | 2006-11-10 | 2008-11-26 | 广州珠江钢铁有限责任公司 | Method for manufacturing 700MPa high-strength weathering steel based on thin slab continuous casting and rolling flow by use of Ti microalloying process |
| CN100419115C (en) * | 2006-11-23 | 2008-09-17 | 武汉钢铁(集团)公司 | Ultrahigh-strength atmospheric-corrosion resistant steel |
| CN100455692C (en) * | 2006-12-08 | 2009-01-28 | 武汉钢铁(集团)公司 | High-strength weathering steel and method of manufacturing same |
| CN101376953B (en) * | 2007-08-28 | 2010-08-11 | 宝山钢铁股份有限公司 | High-corrosion resistant high-strength weather resisting steel and manufacturing method thereof |
| CN101649413B (en) * | 2008-08-15 | 2012-03-28 | 宝山钢铁股份有限公司 | Ultra-strength and high toughness maraging steel and manufacturing method thereof |
| CN101476080B (en) * | 2008-12-26 | 2011-01-26 | 首钢总公司 | Low welding crack sensitivity, quenching and tempering, high rigid plate and manufacturing method thereof |
| CN101928894B (en) * | 2009-06-25 | 2012-09-19 | 宝山钢铁股份有限公司 | High-strength weather resisting steel with Cu2-xS dispersed precipitates and manufacturing method thereof |
| CN101792888A (en) * | 2010-03-17 | 2010-08-04 | 首钢总公司 | High-strength weathering steel and method for producing same |
| CN101875994A (en) * | 2010-03-31 | 2010-11-03 | 湖北猴王焊材有限公司 | Novel weathering resistant steel microalloying compound core-spun yarn |
| CN101875994B (en) * | 2010-03-31 | 2013-12-18 | 湖北猴王焊材有限公司 | Weathering resistant steel microalloying compound core-spun yarn |
| CN101892431A (en) * | 2010-07-07 | 2010-11-24 | 江苏省沙钢钢铁研究院有限公司 | Hot rolled weatherproof bridge steel with yield strength of 500 MPa level and manufacturing method thereof |
| CN102397884A (en) * | 2010-09-16 | 2012-04-04 | 鞍钢股份有限公司 | Method for controlling crazing defect of surface of strip steel in high-Cu steel grade |
| CN102392196A (en) * | 2011-11-15 | 2012-03-28 | 内蒙古包钢钢联股份有限公司 | High-strength high-tenacity rare earth-containing steel material for Z-type steels |
| CN102605287A (en) * | 2012-03-09 | 2012-07-25 | 武汉钢铁(集团)公司 | Steel for high-ductility anti-seismic structure with yield ratio smaller than or equal to 0.70 and production method of steel |
| CN102605287B (en) * | 2012-03-09 | 2013-07-31 | 武汉钢铁(集团)公司 | Steel for high-ductility anti-seismic structure with yield ratio smaller than or equal to 0.70 and production method of steel |
| CN103194695B (en) * | 2013-04-07 | 2015-04-08 | 武汉钢铁(集团)公司 | Steel with stable oxide layer for pretreatment-free high-strength container and manufacture method of steel |
| CN103194695A (en) * | 2013-04-07 | 2013-07-10 | 武汉钢铁(集团)公司 | Steel with stable oxide layer for pretreatment-free high-strength container and manufacture method of steel |
| CN103736945A (en) * | 2013-12-05 | 2014-04-23 | 天水星火机床有限责任公司 | Method for reducing molten iron casting cracks |
| CN105063509A (en) * | 2015-07-27 | 2015-11-18 | 武汉钢铁(集团)公司 | Structural steel with yield strength of 500 MPa for bridges and production method of structural steel |
| CN106222559A (en) * | 2016-08-30 | 2016-12-14 | 南阳汉冶特钢有限公司 | A kind of Novel ocean platform steel steel plate and production method thereof |
| CN106222559B (en) * | 2016-08-30 | 2018-02-13 | 南阳汉冶特钢有限公司 | A kind of offshore platform steel steel plate and its production method |
| CN107365940A (en) * | 2017-08-16 | 2017-11-21 | 北京科技大学 | A kind of preparation method and application of 700MPa levels Ultra-fine Grained high-strength weathering steel |
| CN107365940B (en) * | 2017-08-16 | 2019-11-15 | 北京科技大学 | A kind of preparation method and application of 700MPa grades of Ultra-fine Grained high-strength weathering steel |
| CN109112392A (en) * | 2018-07-17 | 2019-01-01 | 张家港宏昌钢板有限公司 | The high tough high fatigue property Weather-resistance bridge steel plate of TMCP type and preparation method |
| CN109252092A (en) * | 2018-09-30 | 2019-01-22 | 燕山大学 | It is a kind of to exempt from coating weathering steel and preparation method thereof containing rare earth element |
| WO2020237976A1 (en) * | 2019-05-28 | 2020-12-03 | 南京钢铁股份有限公司 | Superfine acicularly-structured structural steel and production method therefor |
| CN112080702A (en) * | 2020-09-16 | 2020-12-15 | 燕山大学 | Weather-resistant bridge steel with impact absorption power of not less than 60J at-60 ℃ in welded coarse grain heat affected zone |
| CN114959451A (en) * | 2022-04-25 | 2022-08-30 | 中国科学院金属研究所 | Weather-resistant and fire-resistant structural steel for south-sea marine environment |
Also Published As
| Publication number | Publication date |
|---|---|
| CN1323187C (en) | 2007-06-27 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN1323187C (en) | Acicular constituent high strength weathering resistant steel and producing method thereof | |
| CN100455692C (en) | High-strength weathering steel and method of manufacturing same | |
| KR102240599B1 (en) | Highly Corrosion-resistant, High Strength, Al-containing Weathering Steel Plate and Process of Manufacturing Same | |
| CN101328564B (en) | Low yield ratio HT780 steel plate having superior weldability and manufacturing method thereof | |
| CN106756517B (en) | A kind of steel plate and its manufacturing method for polar region ship | |
| CN103147017A (en) | Steel plate with high strength and excellent low-temperature toughness and manufacturing method thereof | |
| CN102168229A (en) | Weather resistant steel plate and manufacturing method thereof | |
| CN101892431A (en) | Hot rolled weatherproof bridge steel with yield strength of 500 MPa level and manufacturing method thereof | |
| US20090025839A1 (en) | High tensile strength, refractory steel having excellent weldability and gas cuttability and method for producing same | |
| EP1790749A1 (en) | 490 MPa GRADE HIGH TENSILE STEEL FOR WELDED STRUCTURE EXHIBITING EXCELLENT HIGH TEMPERATURE STRENGTH AND METHOD FOR PRODUCTION THEREOF | |
| KR101623661B1 (en) | Ultra thick steel plate and manufacturing method for offshore structure having ultra-high strength and high toughness | |
| CN101660108A (en) | Non-quenched acicular structure high strength low yield ratio weathering resistant steel and production method thereof | |
| CN102828120A (en) | Strain design based economical pipe line steel and its manufacturing method | |
| CN102534417A (en) | High-performance bridge weathering steel containing Mo and preparation method thereof | |
| CN108624809A (en) | Excellent seawater corrosion resistance, anti-fatigue performance and the brittle ultrahigh-strength steel plates of environment resistant and its manufacturing method | |
| CN107557662B (en) | 800MPa grades of low-cost and easy-to welding thick steel plates of quenching and tempering type and its production method | |
| CN106756612A (en) | A kind of easy laser welding hull plate steel of bainite/martensite/austenite high-ductility and manufacture method | |
| CN1210431C (en) | Steel series with high linear energy and low weld crack sensitivity and its preparing process | |
| KR100660230B1 (en) | Thick steel plate for welded structure having high strength and excellent toughness at the center of thickness and method of producing the same | |
| KR101465088B1 (en) | Low carbon high strength steel plates with good low temperature toughness and manufacturing method for the same | |
| CN102851611B (en) | Ultrahigh toughness steel plate for deep-water pressure resistant shell and manufacture method thereof | |
| CN103667963B (en) | The low-carbon bainite construction(al)steel of a kind of yield tensile ratio < 0.8 and production method | |
| KR101070132B1 (en) | Steel with Excellent Low-Temperature Toughness for Construction and Manufacturing Method Thereof | |
| CN106756478B (en) | A kind of economical seawater corrosion resistance low-density low-alloy steel and preparation method thereof | |
| CN102747284B (en) | High-strength high-tenacity steel for ship structure |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| TR01 | Transfer of patent right | ||
| TR01 | Transfer of patent right |
Effective date of registration: 20180408 Address after: 430083 Qingshan District, Hubei, Wuhan factory before the door No. 2 Co-patentee after: University of Science and Technology Beijing Patentee after: Wuhan iron and Steel Company Limited Address before: 430080 metallurgy Avenue, Qingshan District, Wuhan, Hubei Province, No. 28 Co-patentee before: University of Science and Technology Beijing Patentee before: Wuhan Iron & Steel (Group) Corp. |
|
| CF01 | Termination of patent right due to non-payment of annual fee | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20070627 Termination date: 20201116 |