CN101165202A - High-strength steel with high welding heat influence area toughness and manufacturing method thereof - Google Patents
High-strength steel with high welding heat influence area toughness and manufacturing method thereof Download PDFInfo
- Publication number
- CN101165202A CN101165202A CNA2006100480729A CN200610048072A CN101165202A CN 101165202 A CN101165202 A CN 101165202A CN A2006100480729 A CNA2006100480729 A CN A2006100480729A CN 200610048072 A CN200610048072 A CN 200610048072A CN 101165202 A CN101165202 A CN 101165202A
- Authority
- CN
- China
- Prior art keywords
- rolling
- steel
- temperature
- cooling
- toughness
- 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.)
- Pending
Links
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
The high strength steel with high toughness in the welding heat affected zone has the chemical components including C 0.01-0.04 wt%, Si 0.05-0.6 wt%, Mn 1.5-2.2 wt%, Nb 0.015-0.070 wt%, Ti 0.005-0.03 wt%, B 0.0005-0.005 wt%, Al 0.015-0.07 wt%, Mo 0.2-0.5 wt%, Cu 0.5-1.5 wt%, Ni 0.1-1.0 wt%, Cr 0.3-0.7 wt%, and Fe and inevitable impurity for the rest, and Pcm not higher than 0.3 %. It has one rolling process including the steps of: heating the billet before rolling to 1100-1250 deg.c, re-crystallizing rolling at temperature not lower than 1000 deg.c and in gate deformation of 15-30 %, non-recrystallizing rolling at temperature of 950-750 deg.c and in the accumulated deformation greater than 50 %, naturally cooling to 700-750 deg.c, quick cooling to 500-600 deg.c in the cooling speed of 20-40 deg/s, and air cooling. It has high strength, good low temperature toughness, excellent welding performance, high toughness in the welding heat affected zone and other advantages.
Description
Technical field
The present invention relates to metal material field, relate in particular to a kind of high-strength steel and manufacture method thereof with high welding heat influence area toughness.
Background technology
Low carbon high-strength degree low alloy steel is one of most important structural timber, is widely used among petroleum natural gas pipeline, ocean platform, shipbuilding, bridge, pressurized vessel, building structure, automotive industry, transportation by railroad and the machinofacture.The performance of low carbon high-strength degree low alloy steel own and its welding property depend on the process system of its chemical ingredients, manufacturing processed, wherein intensity, toughness and weldability are the most important performances of low carbon high-strength degree low alloy steel, and its final decision is in the microstructure state of finished steel.In high-strength steel welding in the past, because carbon content is higher, carbon equivalent and crackle sensitivity coefficient are also higher, the crystal grain of welded heat affecting zone is acutely under the effect of Thermal Cycle grows up, the tissue of welded heat affecting zone presents the Wei Shi body, the toughness of welded heat affecting zone has by a relatively large margin decline than mother metal, along with science and technology constantly advances, C in the steel, S, the content of P further reduces, people propose higher requirement to the obdurability and the weldability of steel, promptly the welded heat affecting zone that also has high tenacity when steel plate keeps high tenacity makes the range of application of steel further to promote.
That Japan Nippon Steel company discloses the is by name patent (JP04-346636) of " containing the high manganese super-high strength steel that the HAZ of C, Mn, P, S, Al, B, N, Ni and/or Cu has high tenacity " and the patent (JP2-704810) of " forming the method for MnS compound particles manufacturing large-line energy welding high-strength steel by the complete deoxidation of Al " by name, the inventive point of these two patents all is the large-line energy welding, be crystal grain, reach heat affected zone flexible raising under the large-line energy welding conditions with this by the tiny particle refinement heat affected zone of disperse.Its weak point is that the steel plate of two patents does not all possess low-welding crack-sensitive.
Summary of the invention
For overcoming the deficiencies in the prior art, improve the welding property of high-strength steel in application process, the object of the present invention is to provide a kind of high-strength steel and manufacture method thereof that possesses lower welding crack sensibility and be not less than the mother metal welding heat influence area toughness.
The chemical ingredients (weight percent) that the present invention has the high-strength steel of high welding heat influence area toughness is: C:0.01%～0.04%, Si:0.05%～0.6%, Mn:1.5%～2.2%, Nb:0.015%～0.070%, Ti:0.005%～0.03%, B:0.0005%～0.005%, Al:0.015%～0.07%, Mo:0.2%～0.5%, Cu:0.5%～1.5%, Ni:0.1%～1.0%, Cr:0.3%～0.70%, all the other are Fe and unavoidable impurities.The upper limit of the impurity element in the steel is controlled at P＜0.02%, s＜0.01%, N＜0.006%.The microstructure of steel is ferrite and bainite mixed structure, and satisfies welding crack sensibility indices P cm=C+Si/30+Mn/20+Cu/20+Ni/60+Cr/20+Mo/15+V/10+5B≤0.25%.
The manufacture method of high-strength steel of the present invention comprises smelts and casting, and the operation of rolling adopts the controlled rolling and controlled cooling technology, and the Heating temperature of steel billet in process furnace is 1100～1250 ℃ before being characterized in rolling; Adopt two stage rolling technologies when rolling, carry out according to recrystallize and two stages of non-recrystallization, recrystallize stage rolling temperature 〉=1000 ℃, pass deformation control 15%～30%; Non-recrystallization stage rolling temperature is 950～750 ℃, and the accumulation of distortion amount is greater than 50%; Adopt the two stage types of cooling after the finish to gauge, carry out after rolling treating in 30～100 seconds that temperature, temperature reduce to 700～750 ℃, be chilled to 500～600 ℃ of final cooling temperatures soon with 20～40 ℃/s speed of cooling again, air cooling is to≤200 ℃ afterwards.For the performance of assurance steel is more stable, can carry out temper behind the air cooling, tempering temperature is 500～650 ℃.
Mentality of designing of the present invention is to adopt ladle refining and continuous casting, reduce C, P, the content of S, utilize high temperature non-recrystallization zone controlled rolling to obtain elongated deformed austenite crystal grain, in steel, add a small amount of element that improves hardening capacity, as Mn, Mo, Nb, B, cooling control after rolling condition under, deformed austenite is transformed into the tiny ferrite and the bainite structure of various forms, a large amount of TiNb (the C of uniform distribution in matrix, N) (size is greatly between 10nm-20nm) second phase particle, under the Thermal Cycle high temperature action, reaustenitizing, the second phase particle stops growing up of austenite crystal, under the quick cooling effect of welding, the coarse grain zone forms the Bei Shi ferrite of lath-shaped, bainite forms in the shear mode in process of cooling, produce the many phase transformation dislocation of numbers of poles, even make under the situation of when welding coarse grain zone grain growth, also can make the toughness of coarse grain zone be not less than mother metal, and owing to adopted the Ultra-low carbon design, when welding, do not produce cementite, further improved the toughness of coarse grain zone.The intensity of this steel mainly relies on bainite to strengthen, and adopts the Ultra-low carbon design, and when C＜0.04%, tendency of hardenability is minimum in the steel.
The present invention with the Mn element as principal element, with elements such as Mn, Mo, Cu, Nb, Ti, B to the abundant combined utilization of the effect of welded heat affecting zone bainite transformation, with Cr, Ni as auxiliary element, and combine with rational controlled rolling and controlled cooling production technique, thereby realize the raising of high-strength steel and welding heat influence area toughness, make this steel in the welded heat affecting zone grain growth, also can make the toughness of heat affected zone be not less than mother metal.
The main effect of alloying element in steel that the present invention selects is:
C: carbon is very big to intensity, toughness, the welding property influence of steel, when C＜0.04%, tendency of hardenability is minimum in the steel, but being lower than at 0.01% o'clock, C content can not form enough NbC that in the controlled rolling operation, plays an important role, be difficult to obtain high strength, and cause the toughness of steel to reduce greatly, and welded heat affecting zone is easily softening; Carbon is higher than at 0.06% o'clock, generates Bei Shi ferritic structure minimizing in the tissue in the heat affected zone, and M-A island quantity increases, and toughness is descended, and C is controlled between 0.01%～0.04% in the method.
Mn: manganese is to improve intensity and flexible effective element, and Mn organizes and performance by various mechanism influences in steel.It mainly acts on is solution strengthening, refinement ferrite crystal grain and the hardening capacity that increases steel, and the welded heat affecting zone tissue is had bigger promoter action to bainite transformation, and effect is more remarkable under the low-carbon (LC) condition.
B: boron is the composition of outbalance in the steel, it can improve the hardening capacity of steel, the B solid solution will make in all of steel warm structural transformation postpone strongly in matrix, it and the compound adding of Mo will make steel obtain bainite in very wide cooling rate scope, particularly in soft steel, add the boron of trace, can suppress austenite effectively to ferrite, pearlitic transformation.When being higher than 0.005%, its content can form carbide, so the content of B is generally between 0.0005%～0.005%.
Nb: niobium is the important element in the rolling controlled and cooling controlled steel, it is the austenitic recrystallize of delayed deformation effectively, stops austenite crystal to be grown up, and improves austenite recrystallization temperature, crystal grain thinning, improve intensity and toughness simultaneously, it and micro-boron compound action can be improved hardening capacity significantly, promote bainite transformation, form NbTi (CN) with the compound action of trace Ti, can stop the grain growth in the Thermal Cycle, improve the toughness of welded heat affecting zone.
Ti: adding the titanium of trace, is for the nitrogen element in the fixing steel, thereby guarantees to improve the hardening capacity effect of boron.In the best condition, titanium, nitrogen form titanium nitride, stop steel billet the growing up of crystal grain in heating, rolling, welding process, improve the toughness of mother metal and welded heat affecting zone.Titanium is lower than at 0.0059% o'clock, and nitrogen fixation effect is poor, surpasses at 0.03% o'clock, and nitrogen fixation effect reaches capacity, and superfluous titanium will be assembled in welded heat affecting zone and grows up, and makes the toughness deterioration of steel welded heat affecting zone.
Si: silicon is the bioelement of deoxidation in steel making, adds Si in the steel and can improve purity of steel and deoxidation, and the solid solubility of Si in ferrite is bigger, energy is reinforced ferrite significantly, have certain strengthening effect, when content is lower than 0.05%, be difficult to obtain sufficient deoxidation effect; Content surpasses at 0.6% o'clock, and the degree of cleaning of steel descend, and toughness reduces, and weldability is poor.
A1: aluminium is deoxidant element, can be used as the AlN forming element, crystal grain thinning effectively, and when it contained quantity not sufficient 0.01%, effect was less; Surpass at 0.07% o'clock, desoxydatoin reaches capacity; High more then harmful to mother metal and welding heat influence area toughness.
Mo: molybdenum helps the refinement of austenite crystal when rolling and the generation of fine bainite, and Mo has the solution strengthening effect to ferrite, helps improving the intensity of steel, can remedy the loss of strength that carbon drop brings, but when content surpassed 0.5%, weldability reduced.
Cu: copper is as alloying element, except the precipitation-hardening effect that utilizes Cu is gained in strength, also help the generation that impels the lath-shaped bainite, obtain good low-temperature flexibility, the comprehensive action of Cu and B further improves the welded heat affecting zone hardening capacity of steel, promote the ferritic formation of welded heat affecting zone Bei Shi, adds more copper and also have outstanding erosion resistance and suppress hydrogen and cause that to induce the i.e. effect of anti-HIC of crackle, direct effect be to promote bainite formation.
Ni: nickel significantly improves the toughness of steel, especially low-temperature flexibility, cooperate with elements such as Si, B, Mn simultaneously and can postpone perlitic transformation, make the easier acquisition bainite of steel, the purpose of adding the Ni element in the method mainly is to stop to contain the tendency that the high steel billet of Cu amount cracks when heating or hot rolling.
Cr: chromium reduces bainite start point Bs, helps the acquisition of bainite, but obvious not as Mo to the effect of bainitic transformation.Cr is a carbide forming element, and it promotes ferritic formation, can improve steel strength and toughness.
Realization present method is taked following technical measures on production technique:
Aspect smelting technology, adopt converter smelting, the dark decarburization of top bottom blowing; Adopt the further decarburization of RH vacuum-treat, and carry out microalloying; Ca handles.
On rolling technology, adopt controlled rolling and controlled cooling technology.Billet heating temperature is 1100～1250 ℃ before rolling, and impels alloying element such as Nb to dissolve in austenite, improves austenitic hardenability, helps rolling Bei Shi ferritic formation in heat affected zone in the bainite and welding process in the postcooling process.Adopt recrystallize and non-recrystallization two stages controlled rolling, the recrystallization zone rolling temperature is greater than 1000 ℃, and pass deformation is controlled at 15%～30%, makes the abundant refinement of austenite; Non-recrystallization stage rolling upper temperature limit is controlled at 950 ℃, and lower limit is controlled at 750 ℃, and the accumulation of distortion amount is greater than 50%.The two stage types of cooling are adopted in rolling back, after finish to gauge finishes, carry out waiting in 30～100 seconds, during temperature to 700～750 ℃, enter accelerated cooling device, be cooled to 500～600 ℃ of final cooling temperatures soon with 20～40 ℃/s speed of cooling again, afterwards below the air cooling to 200 ℃, but separate out and can make ferrite generation dynamic recrystallization by the quick heavy reduction rolling strain inducing ultra-fine grained ferrite of continuous multi-pass, thereby obtain the ultra-fine grained ferrite tissue, adopt the acceleration refrigerative type of cooling to cool off fast after the finish to gauge, effectively suppress the alligatoring of strain inducing ferrite.Can be after rolling 500～650 ℃ of tempering, to guarantee the stable performance of steel.
The present invention has adopted with Mn as main alloy element, and valuable alloying element content is few, does not add V element, and is with low cost; This steel grade intensity high and low temperature good toughness, over-all properties is stable, has good welding property, when mother metal has high strength and high tenacity, can obtain to be not less than the toughness of mother metal at welded heat affecting zone, can promote the steel range of application; This steel grade welding crack sensibility is low, does not need preheating before the weldering, and postwelding does not need thermal treatment, can simplify weldprocedure.
Embodiment
For example shown in table 1～table 3, wherein table 1 is the chemical ingredients of embodiment of the invention steel grade to the invention process, and table 2 is the rolling technology of the corresponding embodiment of the present invention, and table 3 is the performance of the corresponding embodiment of the present invention.
The chemical ingredients of table 1 embodiment of the invention
| Embodiment | C | Si | Mn | P | S | Nb | Ti | B | Als | Mo | Cu | Ni | Cr |
| 1 | 0.019 | 0.25 | 2.03 | 0.01 | 0.005 | 0.046 | 0.018 | 0.0012 | 0.031 | 0.27 | 0.55 | 0.32 | 0.31 |
| 2 | 0.018 | 0.24 | 2.04 | 0.01 | 0.004 | 0.050 | 0.016 | 0.0012 | 0.032 | 0.26 | 0.82 | 0.34 | 0.49 |
| 3 | 0.020 | 0.26 | 2.05 | 0.01 | 0.006 | 0.048 | 0.019 | 0.0014 | 0.030 | 0.27 | 0.91 | 0.36 | 0.40 |
| 4 | 0.016 | 0.22 | 2.0 | 0.01 | 0.004 | 0.050 | 0.015 | 0.0013 | 0.030 | 0.22 | 1.06 | 0.58 | 0.31 |
| 5 | 0.014 | 0.20 | 2.02 | 0.01 | 0.005 | 0.048 | 0.016 | 0.0012 | 0.031 | 0.24 | 1.16 | 0.6 | 0.35 |
The rolling technology of table 2 embodiment of the invention
| Embodiment | Heating temperature ℃ | Recrystallize rolling temperature ℃ | Non-recrystallization rolling temperature ℃ | Waiting time s | Speed of cooling ℃/s | Final cooling temperature ℃ | Tempering temperature ℃ |
| 1 | 1230 | ≥1000℃ | 950-780 | 60 | 38 | 550 | 600 |
| 2 | 1240 | ≥1040℃ | 940-780 | 55 | 35 | 570 | |
| 3 | 1200 | ≥1020℃ | 945-790 | 65 | 30 | 560 | 600 |
| 4 | 1180 | ≥1025℃ | 950-795 | 70 | 36 | 560 | |
| 5 | 1210 | ≥1045℃ | 935-800 | 65 | 35 | 550 | 550 |
The performance of table 3 embodiment of the invention
Table 4 and table 5 are the Comparative Examples after the carburetting, and wherein table 4 is the chemical ingredients of Comparative Examples, and table 5 is the performance of Comparative Examples.
The chemical ingredients of table 4 Comparative Examples of the present invention
| Comparative Examples | C | Si | Mn | P | S | Nb | Ti | B | Als | Mo | Cu | Ni | Cr |
| 1 | 0.092 | 0.30 | 1.8 | 0.01 | 0.004 | 0.08 | 0.022 | 0.0012 | 0.035 | 0.25 | 0.64 | 0.43 | 0.29 |
| 2 | 0.086 | 0.35 | 1.8 | 0.01 | 0.008 | 0.07 | 0.024 | 0.0014 | 0.036 | 0.28 | 0.66 | 0.44 | 0.25 |
| 3 | 0.090 | 0.34 | 1.6 | 0.01 | 0.006 | 0.05 | 0.025 | 0.0015 | 0.038 | 0.29 | 0.68 | 0.48 | 0.24 |
The performance of table 5 Comparative Examples of the present invention
From table 4 and table 5, after the enforcement carburetting, steel grade performance in the Comparative Examples and welding property all descend to some extent, and visible carbon content is unsuitable too high, are controlled at more to help improving steel grade performance and welding property thereof in the Ultra-low carbon scope.
Claims (3)
1. high-strength steel with high welding heat influence area toughness, the chemical ingredients (weight percent) that it is characterized in that this steel is: C:0.01%～0.04%, Si:0.05%～0.6%, Mn:1.5%～2.2%, Nb:0.015%～0.070%, Ti:0.005%～0.03%, B:0.0005%～0.005%, Al:0.015%～0.07%, Mo:0.2%～0.5%, Cu:0.5%～1.5%, Ni:0.1%～1.0%, Cr:0.3%～0.70%, surplus is Fe and unavoidable impurities, the microstructure of steel is cable body and bainite mixed structure, and satisfies welding crack sensibility indices P cm=C+Si/30+Mn/20+Cu/20+Ni/60+Cr/20+Mo/15+V/10+5B≤0.25%.
2. the manufacture method of the described high-strength steel of claim 1 comprises and smelting and casting that the operation of rolling adopts the controlled rolling and controlled cooling technology, and the Heating temperature of steel billet in process furnace is 1100～1250 ℃ before it is characterized in that rolling; Adopt two stage rolling technologies when rolling, carry out according to recrystallize and two stages of non-recrystallization, recrystallize stage rolling temperature 〉=1000 ℃, pass deformation is controlled at 15%～30%; Non-recrystallization stage rolling temperature is 950～750 ℃, and the accumulation of distortion amount is greater than 50%; Adopt the two stage types of cooling after the finish to gauge, carry out after rolling treating in 30～100 seconds that temperature, temperature reduce to 700～750 ℃, be chilled to 500～600 ℃ of final cooling temperatures soon with 20～40 ℃/s speed of cooling again, air cooling is to≤200 ℃ afterwards.
3. the manufacture method of high-strength steel according to claim 2 is characterized in that carrying out temper behind the air cooling, and tempering temperature is 480～650 ℃.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNA2006100480729A CN101165202A (en) | 2006-10-19 | 2006-10-19 | High-strength steel with high welding heat influence area toughness and manufacturing method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNA2006100480729A CN101165202A (en) | 2006-10-19 | 2006-10-19 | High-strength steel with high welding heat influence area toughness and manufacturing method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN101165202A true CN101165202A (en) | 2008-04-23 |
Family
ID=39334056
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNA2006100480729A Pending CN101165202A (en) | 2006-10-19 | 2006-10-19 | High-strength steel with high welding heat influence area toughness and manufacturing method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN101165202A (en) |
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102373387A (en) * | 2011-11-02 | 2012-03-14 | 武汉钢铁(集团)公司 | Steel plate for large-strain cold-bent tube and manufacturing method thereof |
| CN101724779B (en) * | 2008-10-21 | 2012-03-28 | 宝山钢铁股份有限公司 | High-tenacity steel and steel plate adaptive to high heat input welding and production method thereof |
| CN102500625A (en) * | 2011-11-21 | 2012-06-20 | 安阳钢铁股份有限公司 | Novel TMCP (Thermal Mechanical Control Process) |
| CN101855379B (en) * | 2008-10-27 | 2012-07-25 | 新日本制铁株式会社 | Fire-resistant steel material with excellent resistance to reheat embrittlement and with low-temperature toughness at welded heat-affected parts, and manufacturing method thereof |
| CN102851615A (en) * | 2011-06-28 | 2013-01-02 | 鞍钢股份有限公司 | Tensile strength 800 MPa grade structure steel plate with low yield ratio and manufacture method thereof |
| CN103320693A (en) * | 2013-06-19 | 2013-09-25 | 宝山钢铁股份有限公司 | Zinc-induced-crack-resistant steel plate and manufacturing method thereof |
| CN104364405A (en) * | 2013-06-13 | 2015-02-18 | 新日铁住金株式会社 | Ultrahigh-tensile-strength steel plate for welding |
| CN104419871A (en) * | 2013-09-05 | 2015-03-18 | 鞍钢股份有限公司 | Steel for welding structure with excellent marine environment corrosion resistance and manufacturing method of steel |
| CN105349888A (en) * | 2015-11-30 | 2016-02-24 | 钢铁研究总院 | High-heat-input welded vanadium nitrogen titanium high-intensity steel plate and preparation method thereof |
| CN106413931A (en) * | 2014-01-22 | 2017-02-15 | Sms集团有限公司 | Method for optimally producing metal steel and iron alloys in hot-rolled and thick plate factories using a microstructure simulator, monitor, and/or model |
| CN110373523A (en) * | 2019-07-16 | 2019-10-25 | 河钢股份有限公司承德分公司 | A kind of 90 feather weight steel for welding wire heat treatment softening method |
-
2006
- 2006-10-19 CN CNA2006100480729A patent/CN101165202A/en active Pending
Cited By (15)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101724779B (en) * | 2008-10-21 | 2012-03-28 | 宝山钢铁股份有限公司 | High-tenacity steel and steel plate adaptive to high heat input welding and production method thereof |
| CN101855379B (en) * | 2008-10-27 | 2012-07-25 | 新日本制铁株式会社 | Fire-resistant steel material with excellent resistance to reheat embrittlement and with low-temperature toughness at welded heat-affected parts, and manufacturing method thereof |
| CN102851615A (en) * | 2011-06-28 | 2013-01-02 | 鞍钢股份有限公司 | Tensile strength 800 MPa grade structure steel plate with low yield ratio and manufacture method thereof |
| CN102373387B (en) * | 2011-11-02 | 2013-05-22 | 武汉钢铁(集团)公司 | Steel plate for large-strain cold-bent tube and manufacturing method thereof |
| CN102373387A (en) * | 2011-11-02 | 2012-03-14 | 武汉钢铁(集团)公司 | Steel plate for large-strain cold-bent tube and manufacturing method thereof |
| CN102500625A (en) * | 2011-11-21 | 2012-06-20 | 安阳钢铁股份有限公司 | Novel TMCP (Thermal Mechanical Control Process) |
| CN104364405A (en) * | 2013-06-13 | 2015-02-18 | 新日铁住金株式会社 | Ultrahigh-tensile-strength steel plate for welding |
| CN103320693A (en) * | 2013-06-19 | 2013-09-25 | 宝山钢铁股份有限公司 | Zinc-induced-crack-resistant steel plate and manufacturing method thereof |
| CN103320693B (en) * | 2013-06-19 | 2015-11-18 | 宝山钢铁股份有限公司 | Anti-zinc fracturing line steel plate and manufacture method thereof |
| CN104419871A (en) * | 2013-09-05 | 2015-03-18 | 鞍钢股份有限公司 | Steel for welding structure with excellent marine environment corrosion resistance and manufacturing method of steel |
| CN106413931A (en) * | 2014-01-22 | 2017-02-15 | Sms集团有限公司 | Method for optimally producing metal steel and iron alloys in hot-rolled and thick plate factories using a microstructure simulator, monitor, and/or model |
| CN105349888A (en) * | 2015-11-30 | 2016-02-24 | 钢铁研究总院 | High-heat-input welded vanadium nitrogen titanium high-intensity steel plate and preparation method thereof |
| CN105349888B (en) * | 2015-11-30 | 2017-06-23 | 钢铁研究总院 | One kind can high heat input welding vanadium nitrogen titanium high-strength steel sheet and preparation method |
| CN110373523A (en) * | 2019-07-16 | 2019-10-25 | 河钢股份有限公司承德分公司 | A kind of 90 feather weight steel for welding wire heat treatment softening method |
| CN110373523B (en) * | 2019-07-16 | 2021-05-11 | 河钢股份有限公司承德分公司 | Heat treatment softening method for steel for 90 kg-grade welding wire |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101165202A (en) | High-strength steel with high welding heat influence area toughness and manufacturing method thereof | |
| CN100372962C (en) | Superhigh strength steel plate with yield strength more than 1100Mpa and method for producing same | |
| CN101736199B (en) | Hot rolling strip steel for high-strength cold forming welding structures and manufacturing method thereof | |
| CN113637917B (en) | 690 MPa-grade ultrahigh-strength extra-thick ship plate steel with excellent low-temperature impact performance and production method thereof | |
| CN111187990B (en) | Hot-rolled H-shaped steel with yield strength of 500MPa and production method thereof | |
| CN111304531B (en) | Hot-rolled H-shaped steel with yield strength of 550MPa and production method thereof | |
| CN100368582C (en) | Ultra-low-carbon bainite steel and producing method thereof | |
| CN101168826A (en) | High-performance low-carbon bainite construction steel and producing method thereof | |
| CN102888565A (en) | High-strength steel plate with yield strength at 690MPa level and manufacture method thereof | |
| CN101619419B (en) | Steel plate for low-carbon high-niobium high strength welding structure and method for manufacturing same | |
| CN110863135A (en) | High-nickel steel for low-temperature container and manufacturing method thereof | |
| CN114411059A (en) | Bridge steel and manufacturing method thereof | |
| CN110343967B (en) | Manufacturing method for obtaining steel plate with uniform longitudinal performance by normalizing rolling | |
| CN114107822B (en) | 15.9-grade high-strength bolt steel and production method and heat treatment method thereof | |
| CN109943771B (en) | High-toughness weldable steel plate with fine grain structure and production method thereof | |
| JPH10265846A (en) | Production of thermally refined high tensile strength steel plate by continuous casting excellent in toughness | |
| CN100350066C (en) | High toughness low carbon bainite thick steel plate and its production method | |
| JP2005281842A (en) | Production method of low temperature service low yield ratio steel material having excellent weld zone toughness | |
| CN109706396A (en) | A kind of nitrogenous low yield strength ratio high-speed rail weathering steel and production method | |
| CN114480949B (en) | 690 MPa-grade low-yield-ratio weather-resistant welding structural steel, steel plate and manufacturing method thereof | |
| CN114737130A (en) | 355 MPa-grade low-temperature steel and manufacturing method thereof | |
| CN101619422A (en) | Steel plate for low-carbon high-niobium extra-high strength welding structure and method for manufacturing same | |
| CN116179956B (en) | Super thick ship plate steel based on same component and achieving different strength levels of 420-890 MPa and production method thereof | |
| CN115181918B (en) | High-strain-strengthening low-yield-ratio pipeline wide and thick plate and production method thereof | |
| CN115505848B (en) | V-Nb-Ti composite microalloyed 500 MPa-165 ℃ low-temperature anti-seismic steel bar and production method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C12 | Rejection of a patent application after its publication | ||
| RJ01 | Rejection of invention patent application after publication |
Open date: 20080423 |