CN102373371B - Method for raising large heat input weldability of thick steel plate - Google Patents
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- CN102373371B CN102373371B CN 201010263961 CN201010263961A CN102373371B CN 102373371 B CN102373371 B CN 102373371B CN 201010263961 CN201010263961 CN 201010263961 CN 201010263961 A CN201010263961 A CN 201010263961A CN 102373371 B CN102373371 B CN 102373371B
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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 high heat input welding performance of thick steel plates.
Background technology
For fields such as shipbuilding, building, pressurized vessel, petroleum natural gas pipeline and ocean platforms, improve the Large Heat Input Welding performance 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.
Behind Large Heat Input 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 (golden swamp high noon, middle Island bright, this Itou Kentaro of Gang, Jin Guyan: enter greatly Hot and weld with high Zhang power Steel material System product System making method, JP5116890,1976.5.28.) in disclosed in the Composition Design of steel, add a certain amount of Ti, N, utilize the TiN particle can suppress the deteriorated of welding heat influence area toughness, weld heat input can be brought up to 50kJ/cm.But when the desired weld heat input of ship 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 ℃, solid solution will partly occur or grow up in the TiN particle, its effect that suppresses the welded heat affecting zone grain growth disappears part, and at this moment it stops the deteriorated effect of welding heat influence area toughness to reduce.
Japanese Patent JP517300 (Xiao Chi is fair, this Inter great it, matsuda is clear one, modern Army doubly rectifies name, just pure, mountain pass Fu Ji in normal times, weld
Hand Hot shadow Ring Bu Tough The ぐ れ Steel Cai System makes method, JP517300,1993.3.8) in disclosed the method for utilizing titanyl compound to improve steel Large Heat Input Welding performance.Titanyl compound is at high temperature stable, is difficult for occuring 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 each other high spud angle crystal grain, be conducive to improve the toughness of welded heat affecting zone.But in the Large Heat Input Welding process of weld heat input greater than 200kJ/cm, depend merely on the toughness that titanyl compound still is not enough to improve welded heat affecting zone.
The bright man of virtue and ability, of Japanese Patent JP3378433 (Infants Island Du Vicinities Righteousness it, thousand 々 rock power are male: weld Hot shadow Ring Bu Tough Gifted れ Steel Ban System making method, 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 the raising along with Mg content in the steel, the quantity of MgO particle increases considerably, in welding process up to 1400 ℃ of whens heating, growing up of austenite crystal is subject to obvious inhibition, and the toughness of welded heat affecting zone is improved significantly.The bright man of virtue and ability, of Japanese Patent JP3476999 (Infants Island Du Vicinities Righteousness it: weld Hot shadow Ring Bu Tough Gifted れ Steel plate, JP3476999,1996.5.21) MgO in the steel is mingled with is divided into that nano level is mingled with (50-500nm) and micron order is mingled with (0.5-5 μ m) two classes, the quantity that this two class is mingled with significantly increases along with increasing of Mg content in the steel, can significantly reduce the particle diameter of austenite crystal, and reduce the size that welded heat affecting zone fragility is organized grain boundary ferrite and ferrite side plate, thereby improve the Large Heat Input Welding performance of Plate Steel.
The purpose of this invention is to provide a kind of method of improving high heat input welding performance of thick steel plates.By to the kind of reductor, interpolation order, the control of oxygen position, addition and addition means when adding, the TiN nanometer precipitate that distributes to form a large amount of disperses.These TiN nanometer precipitates can suppress growing up of welded heat affecting zone austenite crystal, improve the Large Heat Input Welding performance of Plate Steel.
Summary of the invention
The purpose of this invention is to provide a kind of method that improves high heat input welding performance of thick steel plates, by 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 thus growing up of welded heat affecting zone austenite crystal, improve the Large Heat Input Welding performance of slab.
In the present invention, find by a large amount of experimental studies and analyzing and testing that the Mg deoxidized steel can promote nano-TiN particle a large amount of disperse educts in process of setting and phase transition process significantly.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, effectively suppresses Ti
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 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 high heat input welding performance of thick steel plates, 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 sequentially are Mn, Si → Al → Ti → (Ca and/or Mg), 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;
Add the Mg reductor with the form of adding the NiMg alloy in the ingot mould bottom, 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 the speed water-cooled to 350 of 1～30 ℃/s～550 ℃.
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 solution 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 reduce, and are limited to 0.09% on the C.
Si is needed element in the steel-making pre-deoxidation process, when the Si too high levels surpasses 0.3%, 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 is conducive to 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 simultaneously the toughness of welded heat affecting zone, so the content of Mn is 1.3～1.7%,
Ti is by forming Ti
2O
3Particle can promote the ferritic generation of intracrystalline.Simultaneously Ti is combined growing up that generation TiN particle can the pinning austenite crystal with N.So as beneficial element, the lower 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 when content surpasses 0.004%, generates being mingled with of thick oxide compound and sulfide easily.
Cu can improve 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 intensity and the toughness of mother metal, but because it is expensive, in view of the restriction of cost, be 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 determine suitable reductor and interpolation order and method.
The present invention adopts the interpolation of Mn, Si → Al → Ti → (Ca+Mg) sequentially to carry out deoxidation.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 agglomeration, and the removal of floating easily of such inclusion is conducive to improve the cleanliness factor of molten steel.Then after further using Al that the oxygen position is regulated, carry out again the Ti deoxidation.The free oxygen of part is combined 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 the steel medium sulphide content to improve the transverse impact performance of steel, interpolation Ca reductor in the molten steel subsequently.
In tapping process, take to add the Mg reductor in the mode of ingot mould bottom even place mat NiMg alloy at last.Because the NiMg alloy greatly reduces the activity of Mg, evaporation and the oxidational losses of Mg have been reduced.By the alloying of NiMg, also increased the density of Mg additive, reduced its ascent rate, prolonged the solution time of Mg in molten steel.By the stirring action of molten steel impingement flow in the casting cycle, dissolving and the homogenization of composition of Mg in molten steel finished simultaneously in addition.So just can improve significantly the effect of Mg deoxidation.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 saturated greater than the effect of 0.007%, Mg, vaporization losses and the oxidational losses of Mg have been increased 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 ingot mould bottom even place mat NiMg alloy, 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 the inclusion of generating portion particle diameter greater than 5 μ m, these larger inclusiones will as the starting point of crackle, reduce the impelling strength of steel 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 well pinning effect or promote the effect of intracrystalline ferrite 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 generates easily magnesium-aluminium spinel and is mingled with greater than 0.006% the time, is unfavorable for fine disperse distribution the nucleation and growth of inclusion.
The present invention determined the suitable volume density of nanometer precipitate, median size, less than 100nm precipitate proportion.The analysis of nano-precipitation 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 be dissolved, and then use 0.05 μ m Nuclepore membrane filtration, with nano-precipitation be mingled with greatly separating and filtering in two filter membranes.Select 10000 times or above visual field to observe for nano-precipitation, and adopt scanning or probe power spectrum to analyze.By each precipitate is analyzed, can determine size and the chemical constitution of each precipitate.Adopt at last the method for image analysis, by volume density and the size distribution of calculative determination precipitate.
The present invention determines 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 Grain Growth, improves the requirement of slab Large Heat Input Welding performance.
The present invention in rolling and process for cooling,
Heating temperature before rolling is during less than 1050 ℃, the fully solid solution of the carbonitride of Nb.When Heating temperature during greater than 1250 ℃, will cause growing up of austenite crystal.
The breaking down temperature is higher than 950 ℃, and the accumulative total draft is because more than the temperature, recrystallize occurs 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 occur austenite because under such temperature, formed dislocation in the operation of rolling, and the core that can be used as the ferrite 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 speed water-cooled to 350～550 ℃ of the final cooling temperatures of 1～30 ℃/s.When speed of cooling during greater than 30 ℃/s, will reduce the toughness of 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 ℃, will reduce the toughness of mother metal.
Beneficial effect of the present invention:
The present invention takes suitable reductor interpolation order by in smelting and casting process, the addition of control reductor, and by 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 by 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 Heat Input Welding performance of Plate Steel.
Embodiment
The present invention will be further described below in conjunction with embodiment.
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 be dry mixed rear 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 simultaneously CaO.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 with Heating Steel Ingots 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 the speed water-cooled to 350 of 1～30 ℃/s～550 ℃.
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 0.0005-0.007% less than 0.006%, Mg content among the embodiment, 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 the analysis showed that no matter be embodiment or Comparative Examples, the main component of nanometer precipitate all is TiN.Contrast by 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 shows in Comparative Examples, because the Al too high levels is not added again Mg alloy and Fe
2O
3Powder causes precipitation size larger, and the volume density of precipitate is less.
Table 3 has been listed 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 yield strength of mother metal, tensile strength and relative reduction in area are the mean value of two test datas, and mother metal-40 ℃ Charpy-V impact power and welded heat affecting zone-20 ℃ Charpy-V impact power are the mean value of three test datas.
Data can find out that the mother metal mechanical property of embodiment and Comparative Examples does not have obvious difference from table.Be under the condition of 400kJ/cm at weld heat input, test for welded heat affecting zone-20 a ℃ Charpy-V impact power that the value of embodiment 1～5 is respectively 85J, 131J, 119J, 142J, 179J, the value of Comparative Examples 1-2 is 27J, 36J.The impelling strength of embodiment welded heat affecting zone is significantly improved, and can satisfy the requirement of 400kJ/cm Large Heat Input Welding performance.
The invention provides the oxygen position when in smelting and casting process, passing through the control deoxidation, 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 Heat Input Welding performance of Plate Steel.This technology can be used in the manufacturing processed of the Plate Steels such as the deck of boat, building, is used for improving the Large Heat Input Welding performance of Plate Steel.
Claims (2)
1. method that improves high heat input welding performance of thick steel plates, 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 sequentially are Mn, Si → Al → Ti → (Ca and/or Mg), 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;
Add the Mg reductor with the form of adding the NiMg alloy in the ingot mould bottom, 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 the speed water-cooled to 350 of 1～30 ℃/s～550 ℃.
2. the method for raising high heat input welding performance of thick steel plates 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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| KR20170117235A (en) * | 2013-03-26 | 2017-10-20 | 제이에프이 스틸 가부시키가이샤 | High strength thick steel plate with superior brittle crack arrestability and high heat input welding performance and method for manufacturing same |
| CN103215507B (en) * | 2013-04-18 | 2015-01-14 | 湖南华菱湘潭钢铁有限公司 | Steel plate smelting method for improving high heat input welding performance |
| CN105088072B (en) * | 2015-08-27 | 2018-05-25 | 舞阳钢铁有限责任公司 | A kind of high input energy welding steel plate and its production method |
| CN109161671B (en) * | 2018-10-10 | 2020-08-11 | 江阴兴澄特种钢铁有限公司 | High-strength EH36 steel plate for high heat input welding and manufacturing method thereof |
| CN111139336A (en) * | 2020-01-20 | 2020-05-12 | 五矿营口中板有限责任公司 | Deoxidized alloy cored wire for improving welding performance of steel and manufacturing method thereof |
| 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 |
| CN114107828A (en) * | 2020-08-27 | 2022-03-01 | 宝山钢铁股份有限公司 | Steel plate for high-heat-input welding with tensile strength of 570MPa and manufacturing method thereof |
| CN114959510B (en) * | 2021-02-25 | 2023-05-09 | 宝山钢铁股份有限公司 | Thick steel plate with tempering brittleness resistance for high-temperature equipment and manufacturing method thereof |
| 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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