CN1888117A - Ultra-high strength strip steel and its production process - Google Patents
Ultra-high strength strip steel and its production process Download PDFInfo
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Abstract
The ultra-high strength strip steel consists of C 0.10-0.20 wt%, Si<0.6 wt%, Mn not more than 2.6 wt%, Al 0.020-0.080 wt%, Cr 0.35-0.90 wt%, Nb 0.015-0.050 wt%, Ti 0.015-0.050 wt%, and B 0.0005-0.0030 wt%, except Fe and inevitable impurities. Its production process includes the following steps: smelting and casting; hot rolling, acid pickling and cold rolling; continuous annealing and complex roller cooling and gas jetting cooling or high speed gas jetting cooling; and flattening and trimming. It has simplified production process and low production cost.
Description
Technical field
The present invention relates to a kind of ultra-high strength strip steel and production method thereof, particularly 1180Mpa level ultra-high strength strip steel and production method thereof.
Background technology
In recent years; for environment and the save energy of preserving our planet; must reduce automobile fuel consumption; this requires the automobile lightweight; therefore the development requirement of high strength high formability cold-rolled steel sheet steel mill has been proposed; simultaneously, use the demand of the ultrahigh-strength steel more than the 1180Mpa also more and more stronger to multiple automobiles such as collision bumper, door stiffener, crossbeams with strengthening part.
Up to the present, most of strength grade surpasses the main technique that the ultra-high strength strip steel of 1180Mpa commercially produces and is:
Hot rolling → the pickling of steel-making → continuously cast bloom and cold rolling → continuous annealing → pickling → tempering again → smooth → finishing → ultra-high strength strip steel
Wherein continuous annealing operation all adopts the water cooling relevant with water (WQ) or aerosol cooling (ACC) fast cooling method, its continuous annealing process process is for to be heated to cold rolled strip about 800 ℃, insulation certain hour, slow cooling to a certain temperature in shrend equipment with very fast cooling rate cool to room temperature.Water cooling is a kind of method of cheap production high-strength steel, add more a spot of alloying element and also can produce the two-phase of higher-strength grade, heterogeneous and martensite high-strength steel, but this method is when water-cooled, belt steel surface can form one deck iron scale, need once additional pickling, and adopt shrend (WQ) when cooling off fast, under aging temp, stop difficulty of cooling raio, therefore be with steel to have to be cooled to below 100 ℃, so need reheat tempering temperature replenishes tempering, to guarantee the ageing resistance stability of steel band.The main drawback of shrend method at first is to need to increase in addition pickling and reheating equipment, complex manufacturing, and energy consumption is big, cost up and unfavorable to environment protection; Next is that the working of a furnace was relatively poor after the continuous annealing unit of band shrend was produced high-strength steel, be not suitable for producing the product such as automobile exterior panel, household electrical appliances outside plate of great surface quality requirement, super-high strength steel and great surface quality plate all are high value added products, and a continuous annealing unit often production capacity is bigger, and real super-high strength steel actual output and little, far below the great surface quality plate, the production that influences the product of a large amount of great surface qualities for a spot of super-high strength steel is very uneconomic; Be to adopt the cooled band steel of shrend (WQ) at last, because speed of cooling is too fast, inhomogeneous cooling is even and the belt plate shape extreme difference that causes comes very big difficulty for follow-up stable logical strip.And for adopting acceleration aerosol cooling (ACC), though the cooling terminal temperature can be controlled, but contacting back belt steel surface oxidation with water makes follow-up timeliness section working of a furnace difference can not adapt to the thin plate production of great surface quality requirement equally preferably, and final finished all must increase production cost through overpickling and the processing of flash nickel.There are the problems referred to above just because of the method for cooling relevant with water, therefore people all wish to seek out better, the better super-high strength steel production method of comprehensive benefit, so-called dry type (water is not as the heat-eliminating medium) fast cooling method that speed of cooling is hanged down some has slightly caused the attention of iron and steel circle.
Japanese patent application No. spy opens the manufacture method that flat 2-101117 provides the high-strength steel of the good strength grade of a kind of plasticity about the 980Mpa level, Chemical Composition (weight percent) is C:0.12～0.4%, Si:0.3～1.5%, Mn:1.5～3.0%, Al:0.005～0.1%, B:0.0003～0.0050%, the steel of surplus Fe is through hot rolling, after pickling and 35%～80% deflection cold rolling, be heated to that the speed with 1～30 ℃/s is cooled to 300～450 ℃ after 700～850 ℃ of insulations, arrive room temperature at 30 seconds internal cooling after being incubated 15 seconds～10 minutes, obtain having ferrite, the high-strength steel that the plasticity of bainite and residual austenite mixed structure is good.For guaranteeing intensity, the perlite conversion can not take place and directly enter the bainitic transformation district through too fast cold section speed of cooling control in the austenite that forms at two-phase region, its cooling section is longer, there is not the slow cooling section, to plate shape and unfavorable at the logical plate of line stabilization, in addition, the steel of this patent fast cold section speed of cooling too slow (1-30 ℃/S) and do not contain Cr in the composition, Nb, Ti etc. are to strengthening favourable element, can not mainly be contained ferrite and martensitic dual phase steel, because speed of cooling is too low, what this technology obtained probably is the duplex structure that contains ferrite and bainite, or contain ferrite, the heterogeneous structure of bainite and residual austenite, owing to do not have the dispersion-strengthened of martensitic transformation reinforcement and carbonitride so strength grade to be difficult to surpass 1180Mpa, should invent the no smooth operation in annealing back at last, all be disadvantageous to plate shape and the following process of being with steel.
Summary of the invention
The object of the present invention is to provide a kind of new not adopting to use water as heat-eliminating medium, and the method for same energy production high-quality advanced person (based on phase transformation strengthening) ultra-high strength strip steel, pass through phase transformation strengthening, the multiple strengthening mechanism of dispersion-strengthened and solution strengthening improves the intensity of steel and adopts jet cooling and roller is cold or the quick process for cooling of high speed jet on continuous annealing line, obtain ferrite and martensite duplex structure, pure bainite structure or ferrite, the tensile strength of tissue signatures such as martensite and residual austenite and additional dispersion-strengthened particle more than 1180MPa and El be 10～20% super-high strength steel, and need not increase any miscellaneous equipments such as reheat or pickling.
For achieving the above object, the present invention adopts following technical proposals:
Ultra-high strength strip steel, its chemical ingredients is by weight percentage: C:0.10～0.20%, Si＜0.60%, Mn≤2.6%, Al:0.020～0.080%, Cr:0.35～0.90%, Nb:0.015～0.050%, Ti:0.015～0.050%, B:0.0005～0.0030%, surplus is Fe and inevitable impurity.
Further, also contain in N≤0.005%, P≤0.020% and S＜0.015% one or more, by weight percentage.
The production method of ultra-high strength strip steel, it comprises the steps:
A. pressing mentioned component smelts, casts;
B. hot rolling, pickling and cold rolling;
C. continuous annealing, jet method of cooling of roller cold-peace (RC+GJC) or high-speed gas injection cooling (H-GJC) are adopted in the annealing cooling;
D. smooth, finishing.
Further, hot rolling reeling temperature among the step b: 580～660 ℃, cold rolling reduction: 38%～60%.
Soaking temperature in the continuous annealing among the step c: 770～810 ℃, fast cold starting temperature: 560～680 ℃, the band steel is at fast cold section average cooling rate: 20～60 ℃/s, and fast cold final temperature: 270～420 ℃, aging temp≤420 ℃.
Again, smooth unit elongation in the steps d: 0.1～0.4%.
Principle of design of the present invention is as follows:
Consider under the situation that does not adopt the shrend fast-cooling technology, certain independent strengthening mechanism is difficult to make steel to reach the above tensile strength of 1180Mpa, and super-high strength steel of the present invention improves intensity by the multiple strengthening mechanism with phase transformation strengthening, dispersion-strengthened and solution strengthening; On continuous annealing line, do not adopt water as heat-eliminating medium, and adopt " dry type " quick process for cooling of jet cooling of roller cold-peace (RC+GJC) or high speed jet cooling (H-GJC), avoided pickling and reheat operation; By other trace elements, particularly Cr and the B element that adds except that C, Mn the C curve of steel is moved to right, improve the hardening capacity of steel, suitably reduce requirement speed of cooling; Meanwhile we have added the Nb of q.s and the Ti element makes carbide and the nitride that forms Nb and Ti in the steel in steel, thereby produce tangible dispersion-strengthened effect, the adding of Nb and Ti also can be played the effect of tangible crystal grain thinning in addition, improves the intensity and the toughness of material; Optimization and adjustment by Chemical Composition and production technique (steel-making, continuous casting, hot rolling, cold rolling, annealing and smooth) make every mechanical performance index of material satisfy user's requirement.
According to above-mentioned principle of design, we add Nb in steel, Ti forms NbC, NbN, TiN, Ti (C, N), dispersion-strengthened such as TiC and TiS particle, add Cr, B etc. move to right to improve the hardening capacity of steel the C curve of steel, heavy addition Mn, the an amount of Si of interpolation is to improve ferritic intensity in the steel, by control C, P, the content of S is to improve the welding property and the plasticity of steel, strict control O, the content of H is to reduce oxide inclusion and hydrogen induced cracking, cooling by the control continuously cast bloom, adopt hot charging and slab insulation etc. to prevent the measure of slab rimose, raising hot-rolled process parameter particularly hot rolling reeling temperature control precision fluctuates with the mechanical property that reduces hot-rolled sheet, take attenuate hot-rolled sheet thickness, reduce the method for cold rolling reduction and guarantee cold rolling production direct motion, by reducing mouthful kink amount that is retracted into that connects, reduce process section speed, means such as increase strip tension are guaranteed the stable logical plate with steel continuous annealing process, move back soaking temperature by connecting at last, fast cold starting temperature, speed of cooling, fast cold final temperature, the control of key parameter such as aging temp and smooth unit elongation realizes the control to the super-high strength steel structure property.
Describe the effect of each chemical element of super-high strength steel of the present invention and the mentality of designing of technical data below in detail.
At first, C is the austenite stable element, it is again strengthening element, C content low strength is difficult to guarantee, for the intensity that guarantees steel more than 1180Mpa, the content of C must be more than 0.10%, but in order to obtain good welding property and impelling strength, reduce the content of C under the prerequisite of proof strength as far as possible, high-strength steel of the present invention fixes on 0.10～0.20% with C content.
Si is ferritic solution strengthening element, can improve hardening capacity, yet low melting point oxide can appear in the Si too high levels and the welding property of steel is worsened, so generally be no more than 0.8%.Si among the present invention＜0.6%.
Mn is ferritic solution strengthening element, can improve the intensity of ferrite matrix and improve austenitic hardening capacity, can reduce the solid solution C in the ferrite simultaneously, thereby improves the ductility of dual phase steel.Mn is approaching or surpass at 3% o'clock, and processibility descends, Mn among the present invention≤2.6%.
Cr can form dense oxidation film at belt steel surface when improving hardening capacity, improve the solidity to corrosion of steel, minimum addition 0.1%, but the too much affiliation that adds influences its toughness, also can cause spot corrosion, and increase cost, so Cr:0.35 among the present invention～0.90%.
Nb can crystal grain thinning when improving the hardening capacity of steel, strengthening dispersion-strengthened effect, remove the ferrite interstitial atom, make interstitial atom form dispersion-strengthened particles such as NbC, NbN, greatly strongthener intensity and improve ferrite ductility, Nb:0.015 among the present invention～0.050%.
The B of trace just can make the C curve of steel obviously move to right, and significantly improves the hardening capacity of steel, and for being effective, minimum content is 0.0003%, near or surpass at 0.0050% o'clock, the hot workability deterioration of steel, therefore, among the present invention, B:0.0005～0.0030%.
Ti can form TiN, Ti, and (C, N), dispersion-strengthened particles such as TiC and TiS, but therefore crystal grain thinning also simultaneously has tangible strengthening effect, can also improve the welding property of steel simultaneously, Ti:0.015 among the present invention～0.050%.
Al is a deoxidant element, can form AlN particle crystal grain thinning simultaneously.Al is not obvious less than effect in 0.005% o'clock, and surpassing at 0.1% o'clock can increase the inclusion amount, influences plasticity, Al:0.020 among the present invention～0.080%.
The mentality of designing of production technology parameter:
The too high then iron scale of hot rolling reeling temperature can thicken, cause follow-up pickling difficulty, influence production efficiency and product surface quality, coiling temperature is crossed the pearlitic structure of hot-rolled substrate when hanging down with refinement, also bainite even martensitic transformation may take place when if speed of cooling is also high, hot-rolled substrate intensity is increased substantially, influence follow-up cold continuous rolling distortion, so coiling temperature of the present invention is decided to be 580～660 ℃.
Super-high strength steel hot-rolled substrate thickness and precision and surface quality are poor, and cold roller and deformed main purpose is to improve the thickness and precision and the surface quality of material, and deflection hour is difficult to achieve the above object very much.But cold rolling reduction＞60% o'clock, cold rolling process production cost (as roller consumption, power consumption etc.) obviously increases, and plate shape is also worsened.So cold rolling reduction is decided to be 38～60% among the present invention.
The main technique technical parameter of continuous annealing has determined the internal organizational structure and the material mechanical performance of material.High-strength steel application scenario different required weave construction and material capabilities are also different.The present invention by chemical ingredients and production technique particularly organic cooperation of continuous annealing process technical parameter can obtain to be suitable for making the high-strength steel structure structure and the mechanical property of different parts.Following brief description is once:
Connecting the height move back soaking temperature has determined material at high temperature to be in the austenite one phase district or has been in austenite and ferrite two-phase region and this two ratios mutually.For example, the reaming performance that wants to improve material just should improve soaking temperature, so that obtain bainite as much as possible.And want to reduce the yield tensile ratio of material, and the processability that improves material then requires to reduce as far as possible soaking temperature in material two-phase region temperature range, make that final tissue is based on ferrite, and martensite content can not be high.
The height of fast cold starting temperature mainly influences the plate shape of high-strength steel, but its influence factor independently, but relevant with speed of cooling and cooling terminal temperature.Generally speaking fast cold starting temperature height, speed of cooling is fast, and the cooling terminal temperature is low, and then plate shape is relatively poor, but martensitic amount can increase in the material, and the corresponding strength of materials will improve, and plasticity can decrease, and vice versa.Particularly when being lower than the critical cooling velocity of material, speed of cooling can not obtain martensite even bainite, even speed of cooling is higher than critical cooling velocity but will can not obtains martensite equally when the cooling terminal temperature is higher than the Ms point in addition, the cooling terminal temperature then connects bainite when being higher than the Bs point and can not obtain.
The height of aging temp will influence separating out and martensitic decomposition of disperse phase, and generally speaking the aging temp raising can make the strength of materials and hardness descend and the plasticity raising, and vice versa.
The size of smooth unit elongation mainly influences YIELD STRENGTH and plasticity, also can influence plate of material shape.Generally speaking, improve smooth unit elongation material yield intensity will be improved, plasticity descends, and plate shape will make moderate progress, and the limit wave will appear in the serious bending owing to smooth roller when still smooth unit elongation is too big.
The present invention compared with the prior art has conspicuous outstanding feature and advantage:
Ultra-high strength strip steel of the present invention need not to adopt the shrend fast-cooling technology when even moving back production, thereby has also saved follow-up pickling, reheat and flash nickel operation, thereby has reduced production cost and can not influence non-high-strength steel surface quality of products.Contain dispersion-strengthened particle forming element Ti and Nb in its Chemical Composition of super-high strength steel of the present invention and can make element Cr that the C curve of steel significantly moves to right, B etc., but also contain solution strengthening elements such as higher Mn, Si, by the multiple strengthening mechanism complex intensifying of phase transformation strengthening, dispersion-strengthened and solution strengthening, make and to adopt lower speed of cooling to produce the above super-high strength steel of 1180Mpa; The present invention adopts jet compound cooling of roller cold-peace or high speed jet cooling to produce super-high strength steel, does not form iron scale on the surface, does not require additional acid cleaning process, does not also need to reheat and has been aging temp, simplifies technology, saves cost.What the present invention adopted is to be that the master is the schedule of reinforcement of assisting with dispersion-strengthened and solution strengthening with the phase transformation strengthening, heat-eliminating medium is not moisture, adopt jet compound cooling of roller cold-peace or high speed jet refrigerative continuous annealing production technique, adopt this production technique to connect and produce mechanical property under the condition of moving back the existing production unit of unit and the good tensile strength of plate shape is the strong dual phase steel of superelevation more than the 1180MPa, heterogeneous steel, bainite and martensitic steel not changing great majority.
Embodiment
According to the difference of the chemical ingredients, hot rolling of the ultra-high strength strip steel of invention, cold rolling, continuous annealing and flattening technological parameter, the present invention will be further described by embodiment 1～8 below.
The Chemical Composition of molten steel sees Table 1, and surplus is Fe and unavoidable impurities element.
Table 1 embodiment and the chemical ingredients that contrasts patent
| Embodiment | C | Si | Mn | Al | Cr | Nb | Ti | B | N | P | S |
| 1 | 0.15 | 0.5 | 2.5 | 0.04 | 0.50 | 0.025 | 0.015 | 0.0008 | 0.004 | 0.015 | 0.003 |
| 2 | 0.15 | 0.5 | 2.5 | 0.04 | 0.50 | 0.025 | 0.015 | 0.0008 | 0.004 | 0.015 | 0.003 |
| 3 | 0.18 | 0.4 | 2.2 | 0.02 | 0.35 | 0.030 | 0.030 | 0.0018 | 0.003 | 0.018 | 0.004 |
| 4 | 0.10 | 0.6 | 2.6 | 0.08 | 0.90 | 0.015 | 0.049 | 0.0029 | 0.005 | 0.017 | 0.004 |
| 5 | 0.13 | 0.5 | 2.6 | 0.06 | 0.85 | 0.048 | 0.020 | 0.0015 | 0.005 | 0.014 | 0.002 |
| 6 | 0.16 | 0.4 | 2.3 | 0.05 | 0.70 | 0.035 | 0.023 | 0.0005 | 0.004 | 0.019 | 0.002 |
| 7 | 0.20 | 0.3 | 2.1 | 0.05 | 0.40 | 0.040 | 0.020 | 0.0020 | 0.003 | 0.014 | 0.003 |
| 8 | 0.14 | 0.5 | 2.5 | 0.04 | 0.90 | 0.038 | 0.033 | 0.0010 | 0.004 | 0.013 | 0.005 |
| Comparative Examples 1 | 0.31 | 1 | 2 | 0.03 | ---- | ---- | ---- | 0.0021 | 0.003 | 0.006 | 0.004 |
| 2 | 0.31 | 0.2 | 2 | 0.035 | ---- | ---- | ---- | 0.0021 | 0.003 | 0.007 | 0.003 |
Continuous casting steel billet batches after hot rolling, produces ultra-high strength strip steel through CDCM unit (pickling and cold rolling) and CAL unit (continuous annealing and smooth) after the room temperature cooling.Its main technique technical parameter and the finished product mechanical property see Table 2.
Table 2 embodiment and the main technique technical parameter and the product mechanical property that contrast patent
| Embodiment | Slab heating temperature (℃) | Coiling temperature (℃) | Cold rolling draft (%) | Soaking temperature (℃) | Fast cold starting temperature (℃) | Fast speed of cooling (℃/s) | Fast cold terminal temperature (℃) | Aging temp (℃) | Smooth unit elongation (%) | Tensile strength (MPa) | Unit elongation (%) |
| 1 | 1207 | 600 | 41 | 800 | 600 | 53 | 300 | 250 | 0.20 | 1261 | 13 |
| 2 | 1244 | 605 | 41 | 770 | 560 | 36 | 350 | 300 | 0.21 | 1190 | 16 |
| 3 | 1230 | 660 | 60 | 810 | 595 | 60 | 420 | 420 | 0.30 | 1180 | 20 |
| 4 | 1225 | 580 | 38 | 806 | 680 | 51 | 320 | 280 | 0.10 | 1230 | 15 |
| 5 | 1220 | 620 | 42 | 800 | 650 | 45 | 335 | 300 | 0.15 | 1190 | 19 |
| 6 | 1235 | 625 | 42 | 790 | 620 | 40 | 320 | 280 | 0.20 | 1270 | 17 |
| 7 | 1228 | 610 | 40 | 780 | 600 | 20 | 350 | 280 | 0.20 | 1220 | 15 |
| 8 | 1235 | 628 | 42 | 795 | 620 | 35 | 330 | 290 | 0.35 | 1250 | 14 |
| Comparative Examples 1 | ---- | ---- | 65 | 770 | ---- | 10 | 330 | 360 | 0 | 1110 | 24 |
| 2 | ---- | ---- | 65 | 750 | ---- | 10 | 400 | 390 | 0 | 1040 | 21 |
By table 2 as seen, compare with Comparative Examples, the super-high strength steel of this patent adopts jet compound cooling of roller cold-peace or high speed jet cooling to produce when even moving back production, cooling rate is very fast and be convenient to control, by control continuous annealing soaking temperature, fast cold beginning temperature, fast cold final temperature, fast speed of cooling and timeliness temperature, can produce the good tensile strength of mechanical property and plate shape is the above super-high strength steel of 1180MPa, as embodiment 2, by continuous annealing process parameter control (770 ℃ of soaking temperatures, 564 ℃ of fast cold starting temperatures, 350 ℃ of fast cold terminal temperatures, 300 ℃ of aging temps), make the super-high strength steel of production reach tensile strength 1190Mpa, unit elongation 16%, and from chemical ingredients, its C, Mn content is not high, Cr, Nb, Ti, elements such as B add also few.Therefore the production difficulty of operation and little before, and in the continuous annealing operation, it is just much of that fast speed of cooling reaches 36 ℃/s, should much move back unit and all possess this cooling conditions.
Super-high strength steel of the present invention makes and can adopt lower speed of cooling to produce the above super-high strength steel of 1180Mpa by the multiple strengthening mechanism complex intensifying of phase transformation strengthening, dispersion-strengthened and solution strengthening; The present invention adopts jet compound cooling of roller cold-peace or high speed jet cooling to produce super-high strength steel, do not form iron scale on the surface, do not require additional acid cleaning process, do not need to reheat to be aging temp yet, simplify technology, save cost, adopt this production technique to connect and produce mechanical property under the condition of moving back the existing production unit of unit and the good tensile strength of plate shape is the strong dual phase steel of superelevation more than the 1180MPa, heterogeneous steel, bainite and martensitic steel not changing great majority.
Claims (6)
1. ultra-high strength strip steel, its chemical ingredients is by weight percentage:
C 0.10～0.20％，
Si ＜0.60％，
Mn ≤2.60％，
Al 0.020～0.080％，
Cr 0.35～0.90％，
Nb 0.015～0.050％，
Ti 0.015～0.050％，
B 0.0005～0.0030％，
Surplus is Fe and inevitable impurity.
2. ultra-high strength strip steel as claimed in claim 1 is characterized in that, also contains in N≤0.005%, P≤0.020% and S＜0.015% one or more, by weight percentage.
3. the production method of a ultra-high strength strip steel as claimed in claim 1 or 2, it comprises the steps:
A. pressing mentioned component smelts, casts;
B. hot rolling, pickling and cold rolling;
C. continuous annealing, roller cold (RC) and jet GJC are adopted in the annealing cooling) compound method of cooling (RC+GJC) or high-speed gas injection cooling (H-GJC);
D. smooth, finishing.
4. the production method of ultra-high strength strip steel as claimed in claim 3 is characterized in that, hot rolling reeling temperature among the step b: 580～660 ℃, and cold rolling reduction: 38%～60%.
5. the production method of ultra-high strength strip steel as claimed in claim 3, it is characterized in that, soaking temperature in the continuous annealing among the step c: 770～810 ℃, fast cold starting temperature: 560～680 ℃, the band steel is at fast cold section average cooling rate: 20～60 ℃/s, fast cold final temperature: 270～420 ℃, aging temp≤420 ℃.
6. the production method of ultra-high strength strip steel as claimed in claim 3 is characterized in that, smooth unit elongation in the steps d: 0.1～0.35%.
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Family Cites Families (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS59100214A (en) * | 1982-11-29 | 1984-06-09 | Nippon Kokan Kk <Nkk> | Production of thick walled high tension steel |
| JPS6417820A (en) * | 1987-07-13 | 1989-01-20 | Kobe Steel Ltd | Production of electric resistance welded steel tube for heat treatment |
| JP2953638B2 (en) * | 1991-11-01 | 1999-09-27 | 株式会社神戸製鋼所 | Alloyed high-strength hot-dip galvanized steel sheet with excellent plating adhesion and manufacturing method thereof |
| JPH05247534A (en) * | 1992-03-04 | 1993-09-24 | Nippon Steel Corp | Manufacture of cr-series ultra high tensile strength resistance welded steel tube excellent in ductility |
| WO1995004838A1 (en) * | 1993-08-04 | 1995-02-16 | Nippon Steel Corporation | High tensile strength steel having superior fatigue strength and weldability at welds and method for manufacturing the same |
| TW459053B (en) * | 1997-12-19 | 2001-10-11 | Exxon Production Research Co | Ultra-high strength dual phase steels with excellent cryogenic temperature toughness |
| JP2003138340A (en) * | 2001-10-31 | 2003-05-14 | Nippon Steel Corp | Ultrahigh strength steel pipe with excellent toughness of weld zone, and its manufacturing method |
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