CN102373371A - Method for raising large heat input weldability of thick steel plate - Google Patents
Method for raising large heat input weldability of thick steel plate Download PDFInfo
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- CN102373371A CN102373371A CN2010102639613A CN201010263961A CN102373371A CN 102373371 A CN102373371 A CN 102373371A CN 2010102639613 A CN2010102639613 A CN 2010102639613A CN 201010263961 A CN201010263961 A CN 201010263961A CN 102373371 A CN102373371 A CN 102373371A
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Abstract
The invention discloses a method for raising large heat input weldability of a thick steel plate, comprising the following steps: 1) smelting and casting to form a steel plate: adding deoxidizers in the deoxidation process of the liquid steel according to the following types and order: Mn, Si, Al, Ti, and Ca and/or Mg, controlling the initial oxygen place in the liquid steel when Mn deoxidation is carried out in casting, adding Fe2O3 powder to let the oxygen content in the liquid steel be 0.001-0.008 wt%, wherein, the steel plate comprises 0.05-0.09 wt% of C, 0.10-0.30 wt% of Si, 1.3-1.7 wt% of Mn, 0.005-0.02 wt% of Ti, no larger than 0.015 wt% of P, no larger than 0.01 wt% of S, no larger than 0.006 wt% of N, no larger than 0.004 wt% of Ca, and the balance consisting of Fe; in the steel, the volumn density of TiN deposition with the particle size of less than 500 nm is larger than 9.0*107 PCs/mm<3>, the average particle size is less than 80 nm, and the proportion of the deposition with the particle size of less than 100 nm is larger than 75 %; 2) rolling and cooling. The large amount of nano TiN deposition with dispersive distribution formed by the invention can inhibit the growth of austenite crystals in the heat affected zone, and greatly raise the large heat input weldability of the thick steel plate.
Description
Technical field
The invention belongs to ferrous metallurgy and field of iron and steel, particularly a kind of method that improves Plate Steel large-line energy welding property.
Background technology
For fields such as shipbuilding, building, pressurized vessel, petroleum natural gas pipeline and ocean platforms; Improve the large-line energy welding property of Plate Steel; In the time of can improving welding efficiency, shortening worker; Reduce manufacturing cost, the welding heat influence area toughness that therefore improves Plate Steel has become more and more urgent requirement.
After the large-line energy welding, the weave construction of steel is destroyed, and austenite crystal is obviously grown up, and forms the coarse-grain heat affected zone, has reduced the toughness of welded heat affecting zone.Causing the tissue of embrittlement in the coarse-grain heat affected zone is thick grain boundary ferrite, ferrite side plate and the upper bainite that forms in the process of cooling, and closely is close to carbide island M-A constituent element that forms between the perlite of formation, lath at ferrite side plate etc. at grain boundary ferrite.Along with the increase of old austenite crystal particle diameter, the also corresponding increase of grain boundary ferrite and ferrite side plate equidimension, the Charpy-V impact power of welded heat affecting zone will significantly reduce.
Japanese Patent JP5116890 (Kanazawa noon, the island that Kentaro Okamoto, Jingu research: Big into thermal welding of high tensile steel products manufacturing method, JP5116890, 1976.5.28.) in disclosed in the design of the composition of steel, add a certain amount of Ti, N, utilize the TiN particle can suppress the deterioration of welding heat influence area toughness, weld heat input can be brought up to 50kJ/cm.But when the desired weld heat input of deck of boat steel reaches 400kJ/cm; The weld heat input of construction(al)steel reaches under the condition of 800-1000kJ/cm; In welding process, the temperature of welded heat affecting zone will be up to 1400 ℃, and the TiN particle solid solution will partly take place or grows up; Its effect that suppresses the welded heat affecting zone grain growth disappears part, and at this moment it stops the effect of welding heat influence area toughness deterioration to reduce.
Japanese Patent JP517300 (Koike Yun, Honma Hiroyuki Matsuda Shoichi, this army times Zhengming, flat Nakai pure, Yamaguchi Fudge, welding
Hand Full す heat affected zone toughness of steel strongly slightly ta PRODUCING France, JP517300, 1993.3.8) discloses the use of titanium oxides to improve the performance of steel large heat input welding methods.Titanyl compound is at high temperature stable, is difficult for taking place solid solution.The while titanyl compound can be used as ferritic forming core core and plays a role, the refinement ferrite crystal grain, and form the acicular ferrite structure that has high spud angle crystal grain each other, help improving the toughness of welded heat affecting zone.But in the large-line energy welding process of weld heat input, depend merely on the toughness that titanyl compound still is not enough to improve welded heat affecting zone greater than 200kJ/cm.
Japanese Patent JP3378433 (Kagoshima Akihiko, Yoshiyuki Watanabe, thousands 々 rock-hsiung: welding heat affected zone toughness of steel Full gifted slightly ta METHOD FOR PRODUCING, JP3378433, 1996.4.12.) introduced the method that the MgO particulate that utilizes in the steel improves the Plate Steel welding heat influence area toughness; Point out raising along with Mg content in the steel; The quantity of MgO particle increases considerably; Up to 1400 ℃ of whens heating, growing up of austenite crystal receives obvious suppression in welding process, and the toughness of welded heat affecting zone is improved significantly.Japanese Patent JP3476999 (Kagoshima Akihiko, Watanabe Yoshiyuki: welding heat affected zone toughness Full gifted slightly ta steel, JP3476999, 1996.5.21) the steel in the MgO inclusions into nanoscale inclusions (50-500nm) and micron inclusions (0.5-5μm) two, the number of these two types of inclusions in steel with Mg content increased significantly with increasing, can significantly reduce the size of austenite grains and reduce brittleness organization HAZ grain boundary ferrite and the side plate The size of the ferrite, thereby improving the thick steel plate large heat input welding performance.
The purpose of this invention is to provide a kind of method of improving Plate Steel large-line energy welding property.Through to the kind of reductor, interpolation order, the control of oxygen position, addition and addition means when adding, to form the TiN nanometer precipitate that a large amount of disperses distribute.These TiN nanometer precipitates can suppress growing up of welded heat affecting zone austenite crystal, improve the large-line energy welding property of Plate Steel.
Summary of the invention
The purpose of this invention is to provide a kind of method that improves Plate Steel large-line energy welding property; Through in the smelting deoxidation process of steel; The MgO that control forms fine disperse distribution is mingled with; Promotion solidify with phase transition process in bring out and form a large amount of nano TiN precipitates, suppress growing up of welded heat affecting zone austenite crystal thus, improve the large-line energy welding property of slab.
In the present invention, find that the Mg deoxidized steel can promote a large amount of disperses in process of setting and phase transition process of nano TiN particle to separate out significantly through a large amount of experimental studies and analyzing and testing.This be because the formed MgO inclusion of Mg deoxidation to have size little, the characteristics that fine disperse distributes.Like this solidify with phase transition process in, the MgO particle that these fine disperses distribute can be used as the forming core core that TiN separates out and plays a role, and impels separating out in a large number of nano TiN particle.On the other hand, because the avidity of Mg and O is better than the avidity of Al and O greatly, the Mg deoxidized steel can reduce O activity in the steel significantly, suppresses Ti effectively
2O
3Formation, promote separating out of nano TiN particle.Therefore, in the Mg deoxidized steel, promoted separating out in a large number of nano TiN particle, improved the nano TiN particle and suppressed the effect of welded heat affecting zone grain growth, and then improved the toughness of welded heat affecting zone.
For achieving the above object, technical scheme of the present invention is,
A kind of method that improves Plate Steel large-line energy welding property, it comprises the steps:
1) smelt, be cast into ingot, the chemical component weight per-cent of steel plate is: C:0.05～0.09%, Si:0.10～0.30%, Mn:1.3～1.7%; Ti:0.005～0.02%, P≤0.015%, S≤0.01%; N≤0.006%, Ca≤0.004%, surplus Fe and inevitable impurity;
Wherein, add reductor in the steel liquid deoxidation process, reductor kind and interpolation are Mn, Si → Al → Ti → (Ca and/or Mg) in proper order, and Al content weight percent is for being less than or equal to 0.006% in the steel;
Fe is added in initial oxygen position when controlling the Mg deoxidation in the casting cycle in watering ingot mould
2O
3It is 0.001～0.008% that powder makes the oxygen level weight percent in the molten steel;
Form to add the NiMg alloy in the ingot mould bottom adds the Mg reductor, and Mg content weight percent is 0.0005～0.007% in the steel;
In the steel less than the volume density of 500nmTiN precipitate greater than 9.0 * 10
7Individual/mm
3, median size is less than 80nm, less than the shared ratio of 100nm precipitate greater than 75%;
2) rolling and cooling
Ingot casting is heated to 1050～1250 ℃, and the breaking down temperature is higher than 950 ℃, and the accumulative total draft is greater than 30%; Final rolling temperature is less than 950 ℃, and the accumulative total draft is greater than 30%; Then with speed water-cooled to 350～550 of 1～30 ℃/s ℃.
Further, the chemical ingredients of steel plate also contains one or more elements in Cu≤0.3%, Ni≤0.4% or Nb≤0.03%, by weight percentage.
In technical scheme of the present invention,
C, 0.05～0.09%, its lower limit is in order to guarantee near the intensity mother metal and the weld seam, but along with the increase of C content, the toughness of mother metal and welded heat affecting zone and welding property reduction are limited to 0.09% on the C.
Si is a needed element in the steel-making preliminary dexidation process, and the Si too high levels surpasses at 0.3% o'clock, can reduce the toughness of mother metal, and the content of Si is 0.10～0.30%;
Mn can improve the intensity of mother metal, and separating out of MnS helps the ferritic generation of intracrystalline simultaneously, and the lower value of Mn is 1.3%.But too high Mn will cause the center segregation of slab, reduce the toughness of welded heat affecting zone simultaneously, so the content of Mn is 1.3～1.7%,
Ti is through forming Ti
2O
3Particle can promote the ferritic generation of intracrystalline.What simultaneously Ti combined with N that generation TiN particle can the pinning austenite crystal grows up.So as beneficial element, the following of Ti content is limited to 0.005%.But during the Ti too high levels, will impel the generation of TiC, reduce the toughness of mother metal and welded heat affecting zone, thus Ti on be limited to 0.02%;
P, too high levels also will cause center segregation, reduce the toughness of welded heat affecting zone, be limited to 0.015% on the P.
The S too high levels will cause the center segregation of slab, reduce the toughness of mother metal and welded heat affecting zone, be limited to 0.01% on it.
N, content surpasses 0.006%, will cause the solid solution of N, reduces the toughness of mother metal and welded heat affecting zone.
Ca, content surpasses at 0.004% o'clock, generates being mingled with of thick oxide compound and sulfide easily.
Cu can improve the intensity and the toughness of mother metal, but the Cu too high levels will cause hot fragility, be limited to 0.3% on the Cu.
Ni can improve the intensity and the toughness of mother metal, but because it costs an arm and a leg, the restriction in view of cost is limited to 0.4% on it.
Nb, tissue that can the refinement steel improve intensity and toughness, but too high levels will reduce the toughness of welded heat affecting zone, and its upper limit is 0.03%.
For a large amount of nanometer precipitates that form the disperse distribution in steel, at first in the deoxidation process of molten steel, should confirm suitable reductor and interpolation order and method.
The present invention adopts the interpolation of Mn, Si → Al → Ti → (Ca+Mg) to carry out deoxidation in proper order.At first use Si, Mn to carry out deoxidation, can reduce the free oxygen level in the molten steel.Because the oxide compound fusing point that Si, Mn deoxidation form is low, being easy to simultaneously mutually combine forms more low-melting complex inclusion and assembles and grow up, and the removal of floating easily of such inclusion helps improving the cleanliness factor of molten steel.After further using Al that the oxygen position is regulated then, carry out the Ti deoxidation again.The free oxygen of part combines with Ti, forms the oxide compound of Ti, remains in the molten steel.After Si, Mn, Al deoxidation, free oxygen level reduces greatly, so part Ti will be dissolved in the molten steel.For the form of improving sulfide in the steel to improve the transverse impact performance of steel, interpolation Ca reductor in the molten steel subsequently.
In tapping process, take the mode of even place mat NiMg alloy to add the Mg reductor at last in the ingot mould bottom.Because the NiMg alloy greatly reduces the activity of Mg, evaporation and the oxidational losses of Mg have been reduced.Through the alloying of NiMg, also increased the density of Mg additive, reduced its ascent rate, prolonged the solution time of Mg in molten steel.Through the stirring action of molten steel impingement flow in the casting cycle, dissolving and the homogenization of composition of Mg in molten steel accomplished simultaneously in addition.So just can improve the effect of Mg deoxidation significantly.The interpolation order of Ca and Mg can exchange, and also can both add simultaneously.
Mg content in the steel is advisable with 0.0005-0.007%.When Mg content less than 0.0005% the time, the quantity of the microinclusions of generation will significantly reduce, the Mg content in the microinclusions significantly reduces simultaneously, can not satisfy the requirement of separating out TiN at the inclusion spatial induction.If Mg content is greater than 0.007%, the effect of Mg is saturated, has increased vaporization losses and the oxidational losses of Mg simultaneously.
The control of initial oxygen position when Mg adds, making the oxygen level in the molten steel is 0.001%-0.008%.When watering the even place mat NiMg alloy in ingot mould bottom, add the Fe of trace
2O
3Powder is to promote to contain a large amount of formation of MgO microinclusions.When the oxygen level in the molten steel greater than 0.008% the time, with generating the inclusion of part particle diameter greater than 5 μ m, these bigger inclusiones will reduce the impelling strength of steel as the starting point of crackle in the shock test process.When the oxygen level in the molten steel less than 0.001% the time, the quantity not sufficient that will cause fine MgO to be mingled with can not be brought into play pinning effect well or promote the effect of intracrystalline ferritic growth.So the control of initial oxygen position was that to make the oxygen level in the molten steel be 0.001%-0.008% when Mg of the present invention added.
Al content in the steel should be controlled at less than 0.006%.Al content generated magnesium-aluminium spinel easily and is mingled with greater than 0.006% o'clock, was unfavorable for the generation of fine disperse distribution inclusion.
The present invention confirmed the suitable volume density of nanometer precipitate, median size, less than 100nm precipitate proportion.The analysis of fine precipitate in the steel is at first used and decide electric weight non-aqueous solution electrolysis system, and employing 2%TEA nonaqueous electrolytic solution will be tested electrolysis and dissolved, and use 0.05 μ m Nuclepore membrane filtration then, with fine precipitate be mingled with separating and filtering greatly in two filter membranes.Select for use 10000 times or above visual field to observe for fine precipitate, and adopt scanning or probe power spectrum to analyze.Through each precipitate is analyzed, can confirm the size and the chemical constitution of each precipitate.Adopt the method for image analysis at last, through calculating volume density and the size distribution of confirming precipitate.
The present invention confirms in the steel plate that volume density less than the 500nmTiN precipitate is greater than 9.0 * 10
7Individual/mm
3, the median size of precipitate is less than 80nm, less than 100nm precipitate proportion greater than 75%.Such nanometer precipitate can satisfy inhibition welded heat affecting zone austenite crystal grows up, and improves the requirement of slab large-line energy welding property.
The present invention in rolling and process for cooling,
Heating temperature before rolling is during less than 1050 ℃, the solid solution fully of the carbonitride of Nb.When Heating temperature during, will cause growing up of austenite crystal greater than 1250 ℃.
The breaking down temperature is higher than 950 ℃, and the accumulative total draft is because more than the temperature, recrystallize takes place at this greater than 30%, can refine austenite crystal grain.When the accumulative total draft less than 30% the time, forming thick austenite crystal in the heat-processed also can be remaining, has reduced the toughness of mother metal.
Final rolling temperature is less than 950 ℃, and the accumulative total draft is 30-60%, is that recrystallize does not take place austenite because under such temperature, formed dislocation in the operation of rolling, and the core that can be used as the ferritic forming core works.When the accumulative total draft less than 30% the time, formed dislocation is less, is not enough to bring out the forming core of acicular ferrite.
After the finish rolling be because when speed of cooling during less than 1 ℃/s, strength of parent can not meet the demands with 350～550 ℃ of speed water-cooled to the final cooling temperatures of 1～30 ℃/s.When speed of cooling during greater than 30 ℃/s, with the toughness that reduces mother metal.When final cooling temperature during greater than 550 ℃, the intensity of mother metal can not meet the demands.When final cooling temperature during less than 350 ℃, with the toughness that reduces mother metal.
Beneficial effect of the present invention:
The present invention takes suitable reductor interpolation order through in smelting and casting process, the addition of control reductor, and through utilizing interpolation Fe
2O
3The form of powder, the initial oxygen position when accurately controlling the Mg deoxidation forms the MgO that fine disperse distributes through control and is mingled with, promote solidify with phase transition process in induce and form a large amount of nano TiN precipitates.These nano TiN precipitates have suppressed growing up of welded heat affecting zone austenite crystal, have improved the large-line energy welding property of Plate Steel.
Embodiment
Below in conjunction with embodiment the present invention is further specified.
In the present embodiment, smelting procedure carries out in the 50kg vacuum induction furnace.Furnace lining adopts the boric acid of magnesia interpolation 1.2% to do mixed back sintering and forms, and adopts the high alumina ingot mould of anti-the material to cast.In induction furnace, add the 40kg pure iron, add CaO simultaneously.Adopt the mode slag making of the simple CaO of interpolation, guaranteed oxygen position lower in the slag.Heat up when vacuumizing, after furnace charge melted clearly, vacuum tightness can reach 30Pa.To 0.05MPa, adjust the alloying constituent in the molten steel toward the interior filling Ar gas of induction furnace.And the alloy that adds respective element according to the order of Si, Mn, Al, Ti, Ca carries out deoxidation.Sampling and on-line analysis alloying constituent when guaranteeing alloying constituent, are being watered ingot mould bottom interpolation NiMg alloy and Fe at last
2O
3Powder, the NiMg alloy contains Mg 5～50%, and surplus is Ni, and granularity is 1～30mm.
Then steel ingot is heated to 1250 ℃, the breaking down temperature is 1000～1150 ℃, and the accumulative total draft is 50%; Final rolling temperature is 700～850 ℃, and the accumulative total draft is 67%; After the finish rolling with speed water-cooled to 350～550 of 1～30 ℃/s ℃.
The welding heat simulation test utilizes the Gleeble3800 hot modeling test machine to carry out, and peak temperature is 1400 ℃, and the residence time is 3s.t
8/5Time is 383s, and corresponding to the Plate Steel of 50mm specification, weld heat input is 400kJ/cm.
Other processing condition in the Comparative Examples are identical, but Al content is higher, do not add Mg alloy and Fe
2O
3Powder.
Table 1 has been listed the chemical ingredients contrast of embodiment and Comparative Examples.Control Al content is less than 0.006% among the embodiment, and Mg content is 0.0005-0.007%, Fe
2O
3The powder addition is that to make the oxygen level in the molten steel be 0.001%-0.008%.Al content in the Comparative Examples is 0.026% and 0.028%, does not add Mg alloy and Fe
2O
3Powder.
Table 2 has been listed the contrast of nanometer precipitate in embodiment and the Comparative Examples.
Adopt the probe power spectrum to carry out analysis revealed, no matter be embodiment or Comparative Examples, the staple of nanometer precipitate all is TiN.Contrast through nanometer precipitate in embodiment and the Comparative Examples can find that the volume density less than the 500nm precipitate among the embodiment obviously increases, all greater than 9.0 * 10
7Individual/mm
3Median size obviously reduces, all less than 80nm; The ratio shared less than the 100nm precipitate obviously increases, all greater than 75%.
Precipitate in the Comparative Examples less than the volume density of 500nm precipitate all less than 9.0 * 10
7Individual/mm
3, median size is all greater than 80nm, less than the shared ratio of 100nm precipitate all less than 75%.This is illustrated in the Comparative Examples, because the Al too high levels is not added Mg alloy and Fe again
2O
3Powder causes the precipitate size bigger, and the volume density of precipitate is less.
Table 3 has been listed the tensile property and the impelling strength of mother metal in embodiment and the Comparative Examples, and the contrast of the impelling strength of welded heat affecting zone.The ys of mother metal, tensile strength and relative reduction in area are the MV of two test datas, and mother metal-40 ℃ Charpy-V impact power and welded heat affecting zone-20 ℃ Charpy-V impact power are the MV of three test datas.
Data can find out that the mother metal mechanical property of embodiment and Comparative Examples does not have evident difference from table.At weld heat input is under the condition of 400kJ/cm, tests for welded heat affecting zone-20 a ℃ Charpy-V impact power, and the value of embodiment 1～5 is respectively 85J, 131J, 119J, 142J, 179J, and the value of Comparative Examples 1-2 is 27J, 36J.The impelling strength of embodiment welded heat affecting zone is improved significantly, can satisfy the requirement of 400kJ/cm large-line energy welding property.
The invention provides the oxygen position when in smelting and casting process, passing through the control deoxidation, the kind and the addition means of reductor; The MgO that control forms fine disperse distribution is mingled with; Promotion solidify with phase transition process in induce and form a large amount of nano TiN precipitates, improve the method for the large-line energy welding property of Plate Steel.This technology can be used for being used to improve the large-line energy welding property of Plate Steel in the manufacturing processed of Plate Steels such as the deck of boat, building.
Claims (2)
1. method that improves Plate Steel large-line energy welding property, it comprises the steps:
1) smelt, be cast into ingot, the chemical component weight per-cent of steel plate is: C:0.05～0.09%, Si:0.10～0.30%, Mn:1.3～1.7%; Ti:0.005～0.02%, P≤0.015%, S≤0.01%; N≤0.006%, Ca≤0.004%, surplus Fe and inevitable impurity;
Wherein, add reductor in the steel liquid deoxidation process, reductor kind and interpolation are Mn, Si → Al → Ti → (Ca and/or Mg) in proper order, and Al content weight percent is for being less than or equal to 0.006% in the steel;
Fe is added in initial oxygen position when controlling the Mg deoxidation in the casting cycle in watering ingot mould
2O
3It is 0.001～0.008% that powder makes the oxygen level weight percent in the molten steel;
Form to add the NiMg alloy in the ingot mould bottom adds the Mg reductor, and Mg content weight percent is 0.0005～0.007% in the steel;
In the steel less than the volume density of 500nmTiN precipitate greater than 9.0 * 10
7Individual/mm
3, median size is less than 80nm, less than the shared ratio of 100nm precipitate greater than 75%;
2) rolling and cooling
Ingot casting is heated to 1050～1250 ℃, and the breaking down temperature is higher than 950 ℃, and the accumulative total draft is greater than 30%; Final rolling temperature is less than 950 ℃, and the accumulative total draft is greater than 30%; Then with speed water-cooled to 350～550 of 1～30 ℃/s ℃.
2. the method for raising Plate Steel large-line energy welding property as claimed in claim 1 is characterized in that the chemical ingredients of steel plate also contains one or more elements in Cu≤0.3%, Ni≤0.4% or Nb≤0.03%, by weight percentage.
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Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103215507A (en) * | 2013-04-18 | 2013-07-24 | 湖南华菱湘潭钢铁有限公司 | Steel plate smelting method for improving high heat input welding performance |
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Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101153370A (en) * | 2006-09-27 | 2008-04-02 | 鞍钢股份有限公司 | Low-alloy high-strength steel plate capable of being welded at high heat input and manufacturing method thereof |
| CN101724774A (en) * | 2008-10-21 | 2010-06-09 | 宝山钢铁股份有限公司 | Method for adding magnesium in process of manufacturing large heat input welding steel plates |
| CN102191429A (en) * | 2010-03-11 | 2011-09-21 | 宝山钢铁股份有限公司 | Method for improving high heat input welding performance of thick steel plates |
-
2010
- 2010-08-25 CN CN 201010263961 patent/CN102373371B/en active Active
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101153370A (en) * | 2006-09-27 | 2008-04-02 | 鞍钢股份有限公司 | Low-alloy high-strength steel plate capable of being welded at high heat input and manufacturing method thereof |
| CN101724774A (en) * | 2008-10-21 | 2010-06-09 | 宝山钢铁股份有限公司 | Method for adding magnesium in process of manufacturing large heat input welding steel plates |
| CN102191429A (en) * | 2010-03-11 | 2011-09-21 | 宝山钢铁股份有限公司 | Method for improving high heat input welding performance of thick steel plates |
Cited By (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105102651A (en) * | 2013-03-26 | 2015-11-25 | 杰富意钢铁株式会社 | High strength thick steel plate with superior brittle crack arrestability for high heat input welding and method for manufacturing same |
| CN103215507A (en) * | 2013-04-18 | 2013-07-24 | 湖南华菱湘潭钢铁有限公司 | Steel plate smelting method for improving high heat input welding performance |
| CN105088072A (en) * | 2015-08-27 | 2015-11-25 | 舞阳钢铁有限责任公司 | Steel plate for large heat input welding and production method thereof |
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| CN111519098A (en) * | 2020-05-12 | 2020-08-11 | 首钢集团有限公司 | Low-carbon steel and deoxidation method for controlling inclusions in low-carbon steel |
| CN111519098B (en) * | 2020-05-12 | 2021-06-15 | 首钢集团有限公司 | Low-carbon steel and deoxidation method for controlling inclusions in low-carbon steel |
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| CN114645209B (en) * | 2022-03-23 | 2022-10-11 | 新余钢铁股份有限公司 | Steel plate for medium-high temperature pressure vessel and preparation method thereof |
| CN117737595A (en) * | 2024-02-20 | 2024-03-22 | 上海大学 | Steel plate with excellent high heat input welding performance and manufacturing method thereof |
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