CN102191429A - Method for improving high heat input welding performance of thick steel plates - Google Patents
Method for improving high heat input welding performance of thick steel plates Download PDFInfo
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Abstract
The invention discloses a method for improving the high heat input welding performance of thick steel plates. The method comprises the following steps of: 1) smelting and casting to obtain an ingot, wherein deoxidants are added in the deoxidation process of molten steel, the adding sequence of the deoxidants is Mn and Si, Al, Ti, and Ca, a Mg deoxidant is added in the casting process of the molten steel, and the initial oxygen potential during the deoxidation of Mg is accurately controlled by adding Fe2O3 powder into a casting ingot mould; and 2) rolling and cooling. In the method, microfine dispersive distribution and Mg-containing inclusions, which are formed by adding the deoxidants in the deoxidation process of the molten steel and adding the Fe2O3 powder into the casting ingot mould to accurately control the oxygen potential during the deoxidation of the Mg, can inhibit the growth of austenite grains in a welding heat affected zone, and promotes the growth of ferrite in the grains, so that the high heat input welding performance of the thick steel plates is greatly improved.
Description
Technical field
The invention belongs to ferrous metallurgy and field of iron and steel, be specifically related to a kind of method that improves Plate Steel large-line energy welding property.
Background technology
For fields such as shipbuilding, buildings, improve the large-line energy welding property of Plate Steel, can improve welding efficiency, when shortening worker, reduce manufacturing cost.For fields such as pressurized vessel, petroleum natural gas pipeline and ocean platforms, the welding heat influence area toughness that improves Plate Steel has also 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 (golden swamp high noon, middle Island bright, this Itou Kentaro of Gang, Jin Guyan: go into Hot greatly and weld with high Zhang power Steel material System product System making 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 ℃, solid solution will partly take place or grow up in the TiN particle, its effect that suppresses the welded heat affecting zone grain growth disappears major part, at this moment can not stop the deterioration of welding heat influence area toughness.
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, JP517300 has disclosed the method for utilizing titanyl compound to improve steel large-line energy welding property in 1993.3.8).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.
The bright man of virtue and ability, of Japanese Patent JP3378433 (Infants Island Du Vicinities Righteousness it, thousand 々 rock power heros: 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 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 subjected to obvious suppression, 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-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, by in the smelting deoxidation process of steel, form the inclusion of fine disperse distribution and certain ingredients, suppress growing up and promoting the ferritic formation of intracrystalline of welded heat affecting zone austenite crystal, improve the large-line energy welding property of slab.
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%;
Wherein, add reductor in the steel liquid deoxidation process, reductor kind and interpolation are Mn, Si → Al → Ti → Ca in proper order, and Plate Steel Al content weight percent is: less than 0.006%;
In the molten steel casting process, add the Mg-reductor with the form of adding the NiMg alloy in the ingot mould bottom, Plate Steel Mg content weight percent is 0.0005～0.007%;
By in watering ingot mould, adding Fe
2O
3Initial oxygen position when powder is accurately controlled the Mg deoxidation, Fe
2O
3The addition of powder is that to make the oxygen level weight percent in the molten steel be 0.001～0.008%;
The weight in average degree of Mg is more than or equal to 7% in the inclusion of 0.5～10 μ m size in the Plate Steel, and more than or equal to 80%, the inclusion area density is more than or equal to 300/mm less than the inclusion proportion of 3 μ m
2
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%; Subsequently, with speed water-cooled to 350～550 of 1～30 ℃/s ℃.
Further, the chemical ingredients of steel plate also contains one or more in Cu≤0.3%, Ni≤0.4%, Cr≤0.2%, Nb≤0.03% and V≤0.02%, by weight percentage
In technical solution of the present invention,
The lower limit of C 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 a needed element in the steel-making pre-deoxidation process, and its lower value is 0.1%.But the Si too high levels surpasses at 0.3% o'clock, can reduce the toughness of mother metal.
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, thus Mn on be limited to 1.7%.
Ti is by forming Ti
2O
3Particle can promote the ferritic generation of intracrystalline.Simultaneously Ti combines growing up that generation TiN particle can the pinning austenite crystal with N.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.So be limited to 0.02% on the Ti.
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, in view of the restriction of cost, be limited to 0.4% on it.
Cr can improve the intensity of mother metal, but too high levels will reduce toughness, be limited to 0.2% 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%.
V can improve the intensity of mother metal, but too high levels will reduce the toughness of mother metal, and its upper limit is 0.02%.
In order in steel, to form the inclusion that fine disperse distributes, 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 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.Because the oxide compound of Ti has the effect that promotes that the intracrystalline ferrite forms, this helps improving the toughness of welded heat affecting zone.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 to add the Mg reductor at last in the mode of the even place mat NiMg alloy in ingot mould bottom.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 the effect of Mg deoxidation significantly.
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 MnS, TiN on the inclusion surface.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.
Find by the system of analysis carry out to(for) the influence factor of welding heat influence area toughness, carry out under the condition of Mg deoxidation in strictness control initial oxygen position, can promote a large amount of generations of fine disperse distribution inclusion in the steel, play and in welding process, suppress the effect that austenite crystal is grown up.The composition at the microinclusions center of Xing Chenging mainly contains MgO or MgO+Ti simultaneously
2O
3, be the MnS that separates out at its outside surface, help improving the toughness of welded heat affecting zone.
The invention provides the method for initial oxygen position when accurately controlling the Mg interpolation.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 adding Fe
2O
3Powder makes oxygen level in the molten steel greater than 0.008% o'clock, and with the inclusion of generating portion 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 adding Fe
2O
3Powder makes oxygen level in the molten steel less than 0.001% o'clock, and 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 ferrite growth.So Fe of the best of the present invention
2O
3The powder addition is that to make the oxygen level in the molten steel be 0.001%-0.008%.
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 has determined inclusion appropriate ingredients, size and area density.The components utilising SEM-EDS of inclusion measures, and the composition of each specimen holder foreign material is a mean value of choosing the analytical results of inclusion arbitrarily for 10.For sample grind with mirror polish after, utilize SEM under 1500 times multiplying power, to choose the visual field continuously and observe for 50, observed visual field area is greater than 0.27mm
2The distribution of sizes of inclusion and area density are the calculation result of observed inclusion size, quantity and visual field area.The weight in average degree of Mg should be more than or equal to 7% in the 0.5-10 μ m composition of inclusions in the Plate Steel that the present invention determines, less than the inclusion proportion of 3 μ m more than or equal to 80%, the quantity ratio, its area density should be more than or equal to 300/mm
2Such inclusion can satisfy inhibition welded heat affecting zone austenite crystal grows up, and promotes the intracrystalline ferrite to grow up, and improves the requirement of slab large-line energy welding property.
In the rolling and process for cooling of the present invention,
Heating temperature before rolling is during less than 1050 ℃, the solid solution fully of the carbonitride of Nb.When Heating temperature during greater than 1250 ℃, the alligatoring of will growing up of TiN particle can not be played the effect that the pinning austenite crystal is grown up well in welding process.
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 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, will reduce the toughness of mother metal greater than 30 ℃/s.When final cooling temperature during greater than 550 ℃, the intensity of mother metal can not meet the demands.When final cooling temperature during, also will reduce the toughness of mother metal less than 350 ℃.
Beneficial effect of the present invention:
The present invention takes suitable reductor interpolation order by in its smelting process, the addition of control reductor, and pass through utilization and add Fe
2O
3The form of powder, the inclusion that forms small and dispersed distribution and certain ingredients in the steel is impelled in the initial oxygen position when accurately controlling the Mg deoxidation.These inclusiones have suppressed growing up of welded heat affecting zone austenite crystal, have promoted the ferritic growth of intracrystalline, have improved the large-line energy welding property 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 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.
Steel ingot is heated to 1250 ℃ then, 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 does not contain Mg in the inclusion, less than 80%, its area density is less than 300/mm less than the inclusion proportion of 3 μ m
2
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%, does not add Mg alloy and Fe
2O
3Powder.
Table 2 listed the average assay of any 10 0.5-10 μ m inclusiones of embodiment and Comparative Examples, less than the inclusion proportion of 3 μ m and the area density of inclusion.
Being mingled with among the embodiment mainly is to contain MgO or MgO-Ti
2O
3Duplex impurity is found by line sweep and the surface analysis of SEM-EDS, at MgO or MgO-Ti
2O
3Duplex impurity is the inclusion surface of core, has separated out MnS and has been mingled with, and Mg content is more than or equal to 7% in the average assay of inclusion.More than or equal to 80%, its area density is more than or equal to 300/mm less than the inclusion proportion of 3 μ m
2
Inclusion in the Comparative Examples does not contain Mg, is 77.5% less than the inclusion proportion of 3 μ m, and its area density is 178/mm
2This shows in Comparative Examples, because the Al too high levels is not added Mg alloy and Fe again
2O
3Powder causes the inclusion size bigger, and the area density of inclusion 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 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.From the table data as can be seen, the mother metal mechanical property of embodiment and Comparative Examples does not have evident difference.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 is 27J.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 process, passing through the control deoxidation, the kind and the addition means of reductor, form the inclusion of a large amount of fine disperse distributions and certain ingredients, 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%;
Wherein, add reductor in the steel liquid deoxidation process, reductor kind and interpolation are Mn, Si → Al → Ti → Ca in proper order, and Plate Steel Al content weight percent is for being less than or equal to 0.006%;
In the molten steel casting process, add the Mg reductor with the form of adding the NiMg alloy in the ingot mould bottom, Plate Steel Mg content weight percent is 0.0005～0.007%;
By in watering ingot mould, adding Fe
2O
3Initial oxygen position when powder is accurately controlled the Mg deoxidation, Fe
2O
3The addition of powder is that to make the oxygen level weight percent in the molten steel be 0.001～0.008%;
The weight in average degree of Mg is more than or equal to 7% in the inclusion of 0.5～10 μ m size in the Plate Steel, and more than or equal to 80%, the inclusion area density is more than or equal to 300/mm less than the inclusion proportion of 3 μ m
2
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, it is characterized in that, the chemical ingredients of steel plate also contains one or more in Cu≤0.3%, Ni≤0.4%, Cr≤0.2%, Nb≤0.03% and V≤0.02%, by weight percentage.
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN102373371A (en) * | 2010-08-25 | 2012-03-14 | 宝山钢铁股份有限公司 | Method for raising large heat input weldability of thick steel plate |
| CN102560247A (en) * | 2012-01-19 | 2012-07-11 | 武汉钢铁(集团)公司 | Excellent-performance medium plate high-input-energy steel and smelting method thereof |
| CN102605248A (en) * | 2012-03-09 | 2012-07-25 | 宝山钢铁股份有限公司 | Thick steel plates for high heat input welding and production method thereof |
| 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 |
| CN105907920A (en) * | 2016-07-08 | 2016-08-31 | 华北理工大学 | Microalloying method capable of improving performance of steel for large heat input welding |
| EP3395986A4 (en) * | 2015-12-22 | 2019-06-05 | Baoshan Iron & Steel Co., Ltd. | Thick steel plate for high heat input welding and having great heat-affected area toughness and manufacturing method therefor |
| 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 |
| CN115852242A (en) * | 2021-09-24 | 2023-03-28 | 宝山钢铁股份有限公司 | High-temperature high-pressure hydrogen corrosion resistant thick steel plate and manufacturing method thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN102373371A (en) * | 2010-08-25 | 2012-03-14 | 宝山钢铁股份有限公司 | Method for raising large heat input weldability of thick steel plate |
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| EP3395986A4 (en) * | 2015-12-22 | 2019-06-05 | Baoshan Iron & Steel Co., Ltd. | Thick steel plate for high heat input welding and having great heat-affected area toughness and manufacturing method therefor |
| CN105907920A (en) * | 2016-07-08 | 2016-08-31 | 华北理工大学 | Microalloying method capable of improving performance of steel for large heat input welding |
| 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 |
| CN115852242A (en) * | 2021-09-24 | 2023-03-28 | 宝山钢铁股份有限公司 | High-temperature high-pressure hydrogen corrosion resistant thick steel plate and manufacturing method thereof |
| CN115852242B (en) * | 2021-09-24 | 2024-03-08 | 宝山钢铁股份有限公司 | High-temperature high-pressure hydrogen corrosion-resistant thick steel plate and manufacturing method thereof |
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