CN101818304A - Ultra-large linear energy input welding high-strength steel and production method thereof - Google Patents
Ultra-large linear energy input welding high-strength steel and production method thereof Download PDFInfo
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Abstract
The invention discloses ultra-large linear energy input welding high-strength steel and a production method thereof, and solves the problems of high alloying cost, poor welding performance of steel plates and low HAZ impact toughness of the conventional large linear energy input welding high-strength steel. The steel comprises the following chemical compositions in percentage by weight: 0.02 to 0.18 percent of C, 0.10 to 0.60 percent of Si, 0.60 to 1.90 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.010 percent of S, less than or equal to 0.060 percent of Nb, 0.0020 to 0.0060 percent of N, 0.0020 to 0.0060 percent of O, and at least two of 0.005 to 0.030 percent of Ti, less than or equal to 0.010 percent of Ca, less than or equal to 0.010 percent of Mg, 0.0003 to 0.003 percent of B, and 0.008 to 0.015 percent of Ce, and the balance of Fe and inevitable impurities. In addition, the chemical compositions meet the following conditions: (1) 4.0C+Mn is less than or equal to 2.1; (2) the carbon equivalent CE is equal to C+Si/24+Mn/6+Ni/40+Cr/5+Mo/4+V/14 and is less than or equal to 0.39. A casting blank with the compositions is prepared through hot metal desulphurization, converter top and bottom blowing, vacuum deep treatment and fine adjustment of the compositions, the casting blank subjected to controlled rolling is air-cooled to room temperature, and the high-strength strong-toughness and excellent-match steel is obtained. The steel has the advantages of high strength, excellent low temperature toughness, and high Z-direction performance, and can bear ultra-large linear energy input (more than or equal to 500kJ/cm) welding.
Description
Technical field
The present invention relates to a kind of low-carbon and low-alloy high-strength steel, a kind of specifically ultra-large linear energy input welding high-strength steel and production method thereof
Background technology
Quickening along with development and national economy and national basis Facilities Construction speed, each field steel construction maximizes day by day, for further improving welding efficiency, reducing steel construction welding labour intensity and cost of manufacture significantly, the obdurability of the steel plate of making large-scale steel structure and the weld heat input that steel plate can bear are required progressively to improve, for this reason, the technician carries out various improvement to steel plate composition and production method, in the hope of reaching better properties, still still has various deficiencies.
As Japanese Patent JP20070158284 (NIPPON STEEL CORP.HIGH TENSILESTRENGTH STEEL FOR LARGE HEAT INPUT WELDING) and Chinese patent 200710052132 (Wuhan University Of Technologies, a kind of soldering boat deck steel in high intensity by large line energy and manufacture method thereof) all adopt conventional Al deoxidation in the production technique, this deoxidation mode easily produces the Al that worsens steel plate and welded heat affecting zone (HAZ) obdurability
2O
3Inclusion, thus have a strong impact on the welding property of steel plate, and the former also contains precious metal elements such as more relatively Ni, Cr, Mo, V, has increased the alloying cost.
In addition, Chinese patent 200510023216 (Baoshan Iron ﹠ Steel Co., Ltd, but the Plate Steel and the manufacture method of a kind of large-line energy welding) but a kind of Plate Steel of large-line energy welding is disclosed.This invention is started with from alloy designs, adopt the high Mn-Nb micro-alloyed steel of utmost point low-carbon (LC) C-as the basis, suitably control Als content, carry out the B-Mg microalloying, REM handles and metallurgical technology means such as control Ti/N, and optimization TMCP technology, when making the mother metal steel plate low-temperature flexibility that obtains even and excellent, the low-temperature flexibility of HAZ is excellent too during the large-line energy welding.But its shortcoming is that the weld heat input that the steel plate of the micro-alloying technology production adopted can bear is lower, in addition, the high Mn-Nb micro-alloyed steel of utmost point low-carbon (LC) C-for normal when rolling strand to add the temperature of heat request also higher, be unfavorable for energy-saving and emission-reduction.
In addition, document (Li Min, Zheng Xiangzeng.The research overview of large-line energy welding steel, Shandong metallurgy, 2008,30 (3): 8-12) introduced present lot of domestic and foreign iron and steel enterprise and be suitable for large-line energy welding (surpassing 500kJ/cm), had the variety steel of high strength, low-welding crack-sensitive simultaneously in exploitation competitively.The relative steel grade of the present invention of its chemical ingredients is comparatively complicated, and Ni, Cr, Mo, V are precious metal, and alloying cost height has limited use greatly.
Document (Bu Yong, Yin Fazhang etc.Rare earth and Ca, Mg element are to high-strength steel welded heat affecting zone tissue and flexible influence, iron and steel, 2006,41 (4): 71-76) introduced interpolation REM and Ca, Mg element and can in the big line high energy welded heat affecting zone of steel, form the stable oxysulfide (CeCa) of disperse
2O
2S and (CeMg)
2O
2Control the oxysulfide of small and dispersed effectively, obtain the effective grain-size of moderate austenite and the nucleation site that forms intracrystalline acicular ferrite and stabilizing active among the HAZ is provided, promote the collaborative forming core growth of intracrystalline ferrite, make that effectively HAZ organizes miniaturization.Weak point is that the weld heat input that steel plate can bear only is 100kJ/cm, still is difficult to satisfy industrial requirement to high-strength steel ultra-large linear energy input welding property.
Thus, large-scale, super-huge steel construction will face the technology upgrading that need satisfy high-strong toughness energy and ultra-large linear energy input welding property simultaneously and some new problems of technical progress with high-strength steel.
Summary of the invention
The objective of the invention is in order to solve the problems of the technologies described above, a kind of obdurability good match is provided, have intensity height, good low-temperature flexibility, high Z to performance and can bear ultra-large linear energy input (〉=500kJ/cm) steel grade and the production method thereof of welding, the steel plate alloy content of making according to the described production method of the application is low, thereby production cost is low, can be widely used in efficient large-scale, the super-huge steel construction that welds of various needs, and production process is controlled easily, simple to operate, be fit to scale production.
The production method of ultra-large linear energy input welding high-strength steel of the present invention is: with the chemical ingredients of steel by weight percentage ratio count C:0.02～0.18%, Si:0.10～0.60%, Mn:0.60～1.90%, P≤0.015%, S≤0.010%, Nb≤0.060%, N:0.0020～0.0060%, O:0.0020-0.0060%, and Ti:0.005～0.030%, Ca≤0.010%, Mg≤0.010%, B:0.0003-0.003%, among the Ce:0.008-0.015% at least two kinds, all the other inevitably are mingled with for Fe reaches, in addition, above-mentioned chemical ingredients satisfies: (1) 4.0C+Mn≤2.1, (2) carbon equivalent ce (%)=C+Si/24+Mn/6+Ni/40+Cr/5+Mo/4+V/14≤0.39;
Make the strand of above-mentioned composition by desulfurizing iron, converter top and bottom blowing, vacuum depths reason and trimming, carry out controlled rolling and controlled chilling again, air cooling is to room temperature subsequently.
Described deoxidation mode adopts the Si-Mn deoxidation, control tapping oxygen level≤600ppm (quality percentage), Finished Steel oxygen level≤100ppm (quality percentage).
Described controlled rolling method is: start rolling temperature 〉=1200 ℃, three roads, controlled rolling end accumulative total draft 〉=35%, finishing temperature≤870 ℃, preferred 830～870 ℃; Controlling cold mode is: control steel plate speed of cooling 〉=5 ℃/s, steel plate are returned red temperature≤680 ℃, preferred 620～680 ℃, the steel plate air cooling to room temperature, can be checked delivery.
As required, can also with the steel plate air cooling to the room temperature with as-normalized condition delivery, described normalizing process is: normalizing temperature is 890～940 ℃, and soaking time is: 30～40 minutes+thickness of slab (mm) * 1 minute/mm.
Refractory anti-seismic construction steel for high-toughness welding structures of the present invention is to adopt aforementioned production method to make.
High-strength steel of the present invention is with the design of chemical ingredients based on alloying elements such as low C, Si, Mn, be aided with microalloy elements such as Nb, Ti, steel is produced refined crystalline strengthening and precipitation strength effect, reduced the alloying cost simultaneously, reduce production cost, enlarged range of application; Add elements such as micro-B, Ce and Ca, Mg, purify steel and change the form of inclusion; The Ce element that contains can produce Denaturation to inclusion, improves the steel plate mechanical property.Utilize rational rolling technology and thermal treatment process, obtain the High Strength Steel Plate of good obdurability coupling, make steel plate can bear the ultra-large linear energy input welding simultaneously.Nano level Ti that forms in the smelting and/or Mg and/or Ca oxysulfide (OS) high-melting-point particle can stop the welded heat affecting zone grain growth, can also promote the secondary refinement of welded heat affecting zone intergranular structure simultaneously, improve the toughness of large-line energy HAZ jointly.
In the production method, adopted special substitute conventional Al or Fe-Ti alloy or metal Ti with Si-Mn and carry out the deoxidation mode of deoxidation, and clearly stipulated O content in the steel, control tapping oxygen level≤600ppm, the Finished Steel oxygen level is at≤100ppm, thereby avoided Al in the steel
2O
3Harmful be mingled with content, obtain Ti and/or Mg and/or Ca oxysulfide (OS), adopt formula to limit C, Mn total content simultaneously, also carbon equivalent ce has been carried out strict restriction, therefore guaranteed the welding property that steel plate is good.
Utilize controlled rolling to obtain ferrite and add the perlite complex tissue, utilize the composite precipitation effect of separating out of Nb to obtain high strength simultaneously.Steel of the present invention has good obdurability coupling after controlled rolling, have intensity height, good low-temperature flexibility, high Z is to performance and can bear ultra-large linear energy input (〉=500kJ/cm) welding.Utilize steel of the present invention can carry out the welding of methods such as manual metal-arc welding, union-melt weld, shielded welding, electroslag welding or electro-gas welding, can effectively lower welding procedure intensity, improve welding efficiency.Steel of the present invention can be widely used in large-scale, the super-huge steel construction of the efficient welding of various needs.Its market outlook are wide, remarkable in economical benefits.
Steel of the present invention has following advantage:
1. by rational component and proportioning, low alloyed element designs, and the high-strength steel of producing possesses good obdurability coupling, has high strength (R
m〉=590MPa) and good low-temperature flexibility (20 ℃ of Akv 〉=200J).
2. this steel carbon equivalent is lower, the welding property excellence, can bear ultra-large linear energy input (〉=500kJ/cm) welding, under 500kJ/cm large-line energy welding, Charpy V-notch toughness Akv 〉=100J of welded heat affecting zone HAZ in the time of-20 ℃.Can significantly simplify weldprocedure, reduce cost, increase substantially the welding efficiency and the construction speed of product, adapt to big production requirement.
3. the present invention is applied to engineering construction because of having excellent mechanical property and welding property, can improve in-situ production environment, improves operating efficiency 2-5 doubly, ensures construction quality simultaneously, can create huge direct and indirect economic effect, and have good social benefit.
Embodiment
Embodiment 1
In converter, specify the steel of composition in the melting table 1, make strand, adopt Si-Mn, control tapping oxygen level≤600ppm, Finished Steel oxygen level≤100ppm as reductor by desulfurizing iron, converter top and bottom blowing, vacuum depths reason and trimming.With strand be heated to come out of the stove behind 1200～1310 ℃ of abundant austenitizings rolling, the breaking down start rolling temperature is 1200 ℃, last three passages accumulation draft is controlled at 35%, finishing temperature is 830 ℃, carry out the laminar flow cooling after rolling, control steel plate speed of cooling 5 ℃/s, steel plate returns 660 ℃ of red temperature, at last with the steel plate air cooling to room temperature.The thickness of rolled sheet material is 24mm.
Embodiment 2
In the present embodiment, the breaking down start rolling temperature is 1210 ℃, and last three passages accumulation draft is controlled at 40%, and finishing temperature is 850 ℃, 6 ℃/s of control steel plate speed of cooling, and steel plate returns 640 ℃ of red temperature, and all the other are with embodiment 1.The thickness of rolled sheet material is 20mm.
Embodiment 3
In the present embodiment, the breaking down start rolling temperature is 1220 ℃, and last three passages accumulation draft is controlled at 35%, and the finish rolling end temp is 870 ℃, 7 ℃/s of control steel plate speed of cooling, steel plate returns 620 ℃ of red temperature, at last with the steel plate air cooling to room temperature.With as-normalized condition delivery, normalizing temperature is 890～940 ℃ again, and soaking time is: 30～40 minutes+thickness of slab (mm) * 1 minute/mm, all the other are with embodiment 1.The thickness of rolled sheet material is 22mm.
Embodiment 4
In the present embodiment, the breaking down start rolling temperature is 1230 ℃, and last three passages accumulation draft is controlled at 40%, and finishing temperature is 860 ℃, and steel plate returns 680 ℃ of red temperature, and all the other are with embodiment 1.The thickness of rolled sheet material is 24mm.
Embodiment 5
In the present embodiment, the breaking down start rolling temperature is 1210 ℃, and the finish rolling start rolling temperature is 900 ℃, and last three passages accumulation draft is controlled at 40%, and finishing temperature is 865 ℃, 5 ℃/s of control steel plate speed of cooling, and steel plate returns 650 ℃ of red temperature, and all the other are with embodiment 1.The thickness of rolled sheet material is 18mm.
Embodiment 6
In the present embodiment, the breaking down start rolling temperature is 1220 ℃, and the finish rolling start rolling temperature is 980 ℃, and last three passages accumulation draft is controlled at 35%, and the finish rolling end temp is 840 ℃, and steel plate returns 675 ℃ of red temperature, and all the other are with embodiment 3.The thickness of rolled sheet material is 16mm.
Comparative example 1～comparative example 3 is the steel plates that adopt the ordinary method utilization to make strand, and the deoxidation mode adopts conventional Al deoxidation.
The embodiment of the invention 1～6 sees Table 1 with the chemical ingredients of comparative example 1～3.
The chemical ingredients (wt%) of table 1 steel of the present invention and comparative steel
The performance of table 2 embodiment of the invention steel plate and comparative example steel plate
| Grade of steel | ??R eL/MPa | ??R m/MPa | ??A/％ | Steel plate toughness/J | HAZ toughness/J |
| Implement 1 | ??430 | ??595 | ??21 | ??237 | ??107 |
| Implement 2 | ??425 | ??615 | ??20 | ??220 | ??119 |
| Implement 3 | ??435 | ??605 | ??21 | ??258 | ??115 |
| Implement 4 | ??420 | ??595 | ??23 | ??248 | ??116 |
| Implement 5 | ??430 | ??600 | ??22 | ??244 | ??110 |
| Implement 6 | ??460 | ??630 | ??21 | ??249 | ??112 |
| Comparative example 1 | ??430 | ??615 | ??19 | ??245 | ??9 |
| Comparative example 2 | ??420 | ??590 | ??21 | ??249 | ??7 |
| Comparative example 3 | ??425 | ??600 | ??20 | ??253 | ??10 |
In the table 2, the Charpy V-notch toughness of steel plate when steel plate toughness is-20 ℃; The Charpy V-notch toughness of HAZ when HAZ toughness is-20 ℃ of 550kJ/cm large-line energy thermal analogy welding backs.As can be seen from Table 2, steel normal temperature yield strength ReL that the embodiment of the invention makes and tensile strength Rm and comparative example are in same level, and unit elongation A is better than compared steel slightly.In addition, before 550kJ/cm large-line energy welding heat simulation test, the impelling strength of present embodiment steel-20 ℃ and comparative example steel are in same level-20 ℃ impelling strength, but after 550kJ/cm large-line energy welding heat simulation, the HAZ impelling strength of inventive embodiments steel-20 ℃ is higher than the comparative example steel far away.
As can be seen from Table 1, the inventive embodiments steel adopts the composite oxygen sulfide of Ti and/or Ca and/or Mg and/or B and/or Ce to obtain Chinese People's Anti-Japanese Military and Political College's heat input (〉=500kJ/cm) welding property in composition design, by reducing carbon and special microalloying, improve the purity of steel simultaneously, thereby guarantee that this steel has good low-temperature flexibility.Steel of the present invention all can be implemented at each smelter, can improve the welding efficiency of large-scale steel structure greatly, reduces manufacturing cost.Steel of the present invention can be widely used in large-scale, the super-huge steel construction of the efficient welding of various needs.Its remarkable in economical benefits, market outlook are very wide.
Claims (5)
1. the production method of a ultra-large linear energy input welding high-strength steel, it is characterized in that, with the chemical ingredients of steel by weight percentage ratio count C:0.02～0.18%, Si:0.10～0.60%, Mn:0.60～1.90%, P≤0.015%, S≤0.010%, Nb≤0.060%, N:0.0020～0.0060%, O:0.0020-0.0060%, and Ti:0.005～0.030%, Ca≤0.010%, Mg≤0.010%, B:0.0003-0.003%, among the Ce:0.008-0.015% at least two kinds, all the other inevitably are mingled with for Fe reaches, in addition, above-mentioned chemical ingredients satisfies: (1) 4.0C+Mn≤2.1, (2) carbon equivalent ce (%)=C+Si/24+Mn/6+Ni/40+Cr/5+Mo/4+V/14≤0.39;
Make the strand of above-mentioned composition by desulfurizing iron, converter top and bottom blowing, vacuum depths reason and trimming, carry out controlled rolling and controlled chilling again, air cooling is to room temperature subsequently.
2. the production method of ultra-large linear energy input welding high-strength steel as claimed in claim 1 is characterized in that, described deoxidation mode adopts the Si-Mn deoxidation, control tapping oxygen level≤600ppm, Finished Steel oxygen level≤100ppm.
3. the production method of ultra-large linear energy input welding high-strength steel as claimed in claim 1 or 2 is characterized in that, described controlled rolling method is: start rolling temperature 〉=1200 ℃, three roads, controlled rolling end accumulative total draft 〉=35%, finishing temperature≤870 ℃; The controlled chilling mode is: control steel plate speed of cooling 〉=5 ℃/s, steel plate are returned red temperature≤680 ℃.
4. the production method of ultra-large linear energy input welding high-strength steel as claimed in claim 3, it is characterized in that, with the steel plate air cooling to the room temperature with as-normalized condition delivery, described normalizing process is: normalizing temperature is 890～940 ℃, and soaking time is: 30～40 minutes+thickness of slab (mm) * 1 minute/mm.
5. a refractory anti-seismic construction steel for high-toughness welding structures is characterized in that, adopts each described production method among the claim 1-4 is prepared from.
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Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103422021A (en) * | 2013-09-13 | 2013-12-04 | 武汉钢铁(集团)公司 | Low-yield-ratio structural steel with yield ratio equal to or larger than 550MPa and manufacturing method thereof |
| CN104561779A (en) * | 2014-12-04 | 2015-04-29 | 昆明理工大学 | Q550-grade earthquake-resistant steel and method for producing Q550-grade earthquake-resistant steel by using steekle mill |
| CN104630655A (en) * | 2014-11-28 | 2015-05-20 | 武汉钢铁(集团)公司 | Extra-thick steel plate having excellent balance between strength and toughness and used for welded structure and production process thereof |
| CN105821325A (en) * | 2016-06-15 | 2016-08-03 | 山东钢铁股份有限公司 | Tempered high-low-temperature toughness pipeline steel and manufacturing method |
| JP2018193595A (en) * | 2017-05-19 | 2018-12-06 | 新日鐵住金株式会社 | Carbon steel cast slab and manufacturing method of carbon steel cast slab |
| WO2022171081A1 (en) * | 2021-02-09 | 2022-08-18 | 宝山钢铁股份有限公司 | Steel for hull structure resistant to collision and rupture, and manufacturing method therefor |
| CN115029635A (en) * | 2022-06-21 | 2022-09-09 | 湖南华菱湘潭钢铁有限公司 | Large heat input welding high-strength storage tank steel plate and production method thereof |
| CN115216683A (en) * | 2022-05-19 | 2022-10-21 | 北京科技大学 | Method for regulating and controlling ferrite form in casting blank tissue and prepared microalloyed steel |
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|---|---|---|---|---|
| CN103422021A (en) * | 2013-09-13 | 2013-12-04 | 武汉钢铁(集团)公司 | Low-yield-ratio structural steel with yield ratio equal to or larger than 550MPa and manufacturing method thereof |
| CN103422021B (en) * | 2013-09-13 | 2015-07-08 | 武汉钢铁(集团)公司 | Low-yield-ratio structural steel with yield ratio equal to or larger than 550MPa and manufacturing method thereof |
| CN104630655A (en) * | 2014-11-28 | 2015-05-20 | 武汉钢铁(集团)公司 | Extra-thick steel plate having excellent balance between strength and toughness and used for welded structure and production process thereof |
| CN104561779A (en) * | 2014-12-04 | 2015-04-29 | 昆明理工大学 | Q550-grade earthquake-resistant steel and method for producing Q550-grade earthquake-resistant steel by using steekle mill |
| CN104561779B (en) * | 2014-12-04 | 2017-06-13 | 昆明理工大学 | A kind of Q550 grades of shock resisting steel and with steekle mill produce the Q550 grades of method of shock resisting steel |
| CN105821325A (en) * | 2016-06-15 | 2016-08-03 | 山东钢铁股份有限公司 | Tempered high-low-temperature toughness pipeline steel and manufacturing method |
| JP2018193595A (en) * | 2017-05-19 | 2018-12-06 | 新日鐵住金株式会社 | Carbon steel cast slab and manufacturing method of carbon steel cast slab |
| WO2022171081A1 (en) * | 2021-02-09 | 2022-08-18 | 宝山钢铁股份有限公司 | Steel for hull structure resistant to collision and rupture, and manufacturing method therefor |
| CN115216683A (en) * | 2022-05-19 | 2022-10-21 | 北京科技大学 | Method for regulating and controlling ferrite form in casting blank tissue and prepared microalloyed steel |
| CN115029635A (en) * | 2022-06-21 | 2022-09-09 | 湖南华菱湘潭钢铁有限公司 | Large heat input welding high-strength storage tank steel plate and production method thereof |
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