CN102605248A - Thick steel plates for high heat input welding and production method thereof - Google Patents
Thick steel plates for high heat input welding and production method thereof Download PDFInfo
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Abstract
Disclosed are thick steel plates for high heat input welding and a production method thereof. The method includes the steps: firstly, smelting, refining and continuous casting; adding deoxidizer in deoxidation of molten steel according to a sequence of Mn, Si, Al and Ti; finally adding Ca and/or RE deoxidizer, adding Fe2O3 powder to accurately control an initial oxygen level in Ca and/or RE deoxidation of the molten steel; secondly, rolling; and thirdly cooling, wherein molten steel comprises, in weight percentage, 0.05-0.09% of C, 0.10-0.30% of Si, 1.3-1.7% of Mn, 0.005-0.03% of Ti, 0.003-0.025% of Nb, 0.001-0.01% of S, not more than 0.05% of P, not more than 0.006% of N, 0.0005-0.001% of Al, 0.0005-0.004% of Ca, not more than 0.01% of RE, the balance of Fe, and unavoidable impurities. Fine scattered Ca and/or RE oxide and sulfide inclusions can be formed, ratios of (Ca+RE)/Al, Ti/Al and (Ca+RE)/Mn in the inclusions are reasonably controlled, growth of intra-granular ferrite in a welding heat affected zone is promoted, and the performance of high heat input welding of the thick steel plates can be improved greatly.
Description
Technical field
The invention belongs to ferrous metallurgy and field of iron and steel, particularly a kind of large heat input welding steel plates and method of manufacture thereof.
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 welded heat affecting zone steel is destroyed, and austenite crystal is obviously grown up, and forms the coarse grain zone.The tissue that causes embrittlement in the coarse grain zone is ferrite side plate, the upper bainite that forms in the process of cooling, thick grain boundary ferrite and closely be close to carbide island martensite body-austenite constituent element that forms between the perlite of formation, lath at ferrite side plate etc. at grain boundary ferrite.Increase along with weld heat input; It is big that the original austenite grain particle diameter becomes, and ferrite side plate and upper bainite are organized flourishing more, the also corresponding increase of the size of grain boundary ferrite; The Charpy-V impact power of welded heat affecting zone will significantly reduce, and this has reduced the toughness of welded heat affecting zone.
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 jointed hands heat affected zone toughness Full す strongly slightly ta steel 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, Watanabe righteous, thousands
Rock Force male: 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.
Summary of the invention
The purpose of this invention is to provide a kind of large heat input welding steel plates and method of manufacture thereof; Through in the deoxidation process of steel-making; To the kind of reductor, interpolation order, the control of oxygen position, addition and addition means when adding, optimize the composition design of alloying element, and select to generate the inclusion of suitable component; Suppress growing up and promoting the ferritic growth of intracrystalline of welded heat affecting zone austenite crystal, thereby improve the large-line energy welding property of Plate Steel.
For achieving the above object, technical scheme of the present invention is:
A kind of large heat input welding steel plates, its chemical component weight per-cent is: C 0.05～0.09%, and Si 0.10～0.30%; Mn 1.3～1.7%, and Ti 0.005～0.03%, and Nb 0.003～0.025%; S:0.001～0.01%, P≤0.015%, N≤0.006%; Al 0.0005～0.02%, and Ca 0.0005～0.004%, RE≤0.01%; All the other are Fe and inevitable impurity;
Wherein, In the steel in the inclusion of particle diameter more than or equal to 1.0 μ m; (Ca+RE)/and the ratio of Al weight percent content is more than or equal to 0.3, and the ratio of Ti/Al weight percent content is more than or equal to 0.15, (Ca+RE)/ratio of Mn weight percent content is 0.25～2.5.
Further, the chemical ingredients of steel also contains more than one elements in Cu≤0.3%, Ni≤0.4% or B≤0.002%, by weight percentage.
Again, in the steel weight percent ratio of Ti/Nb more than or equal to 1.1.
The method of manufacture of large heat input welding steel plates of the present invention comprises the steps:
1) smelting, refining and continuous casting
The chemical component weight per-cent of steel is: C 0.05～0.09%, and Si 0.10～0.30%, and Mn 1.3～1.7%; Ti 0.005～0.03%, and Nb 0.003～0.025%, S:0.001～0.01%; P≤0.015%, N≤0.006%, Al 0.0005～0.02%; Ca 0.0005～0.004%, RE≤0.01%; All the other are Fe and inevitable impurity;
Wherein, in the steel liquid deoxidation process, add reductor, reductor kind and interpolation are in proper order: Mn, Si → Al → Ti;
Mode through adding SiCa alloy and/or rare earth ferrosilicon adds Ca and/or RE reductor;
Through adding Fe
2O
3Initial oxygen position when powder is controlled Ca and/or RE deoxidation, Fe
2O
3The addition of powder is that to make the oxygen level weight percent in the molten steel be 0.001～0.01%;
In the steel in the inclusion of particle diameter more than or equal to 1.0 μ m; (Ca+RE)/ratio of Al weight percent content is more than or equal to 0.3; The ratio of Ti/Al weight percent content is more than or equal to 0.15, (Ca+RE)/and the ratio of Mn weight percent content is 0.25～2.5;
2) rolling
Strand is heated to 1050～1250 ℃, and the breaking down temperature is higher than 930 ℃, and the accumulative total draft is greater than 30%; Final rolling temperature is less than 930 ℃, and the accumulative total draft is greater than 30%;
3) cooling
With 300～550 ℃ of rate of cooling water-cooled to the final cooling temperatures of 2～30 ℃/s.
Further, the chemical ingredients of steel also contains more than one elements in Cu≤0.3%, Ni≤0.4% or B≤0.002%, by weight percentage.
Again, in the steel weight percent ratio of Ti/Nb more than or equal to 1.1.
In the composition design of steel of the present invention:
C is the element that increases steel strength, and in order to guarantee the necessary intensity of Plate Steel mother metal, the following of C content is limited to 0.05%.But excessively add C, will cause the toughness of mother metal and welded heat affecting zone to reduce, C is last to be limited to 0.09%.
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 in the large-line energy welding process, the generation with promoting island martensite body-austenite constituent element significantly reduces welding heat influence area toughness simultaneously.Si content is 0.10～0.30%.
Mn can be used as the preliminary dexidation element again and play a role through the intensity of solution strengthening raising mother metal.Separating out of MnS can promote 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 Mn content 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, so the Ti upper content limit is 0.03%.
Nb, tissue that can the refinement steel improves intensity and toughness, and its lower limit is 0.003%.But too high levels will reduce the toughness of welded heat affecting zone, and its upper limit is 0.025%.
The present invention also finds, can promote separating out of TiN particle effectively through the ratio that improves Ti/Nb, suppresses separating out of NbN particle.Utilizing Ca and/or RE to carry out in the process of deoxidization desulfuration; The TiN particle is separated out on the oxide compound of Ca and/or RE and the surface of sulfide particles easily; Such TiN particle can suppress growing up of austenite crystal in the Thermal Cycle process, promote the ferritic growth of intracrystalline.The present invention further proposes Ti/Nb ratio more than or equal to 1.1.
S in the interpolation process of Ca and/or RE, forms sulfide with Ca and/or RE, can also promote MnS further separating out on Ca and/or RE sulfide particles, thereby promote the ferritic formation of intracrystalline, is limited to 0.001% under it.But its too high levels will cause the center segregation of slab, reduce the toughness of mother metal and welded heat affecting zone, on be limited to 0.01%.
P is the impurity element in the steel, should reduce as far as possible.Its too high levels will cause center segregation, reduce the toughness of welded heat affecting zone, be limited to 0.015% on the P.
N, content surpasses 0.006%, will cause the solid solution of N, reduces the toughness of mother metal and welded heat affecting zone.
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.
B through improving the hardening capacity of steel, can improve the intensity of steel.But will cause hardening capacity significantly to rise during too high levels, and reduce the toughness of mother metal, its upper limit is 0.002%.
In method of manufacture of the present invention, the present invention adopts the interpolation of Mn, Si → Al → Ti → Ca and/or RE 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.
Al content in the steel should be controlled at 0.0005～0.02%.Al content generated bunch shape alumina inclusion easily greater than 0.02% o'clock, was unfavorable for the generation of fine disperse distribution inclusion.
Add Ca and RE reductor through the mode of adding SiCa alloy and/or rare earth ferrosilicon alloy at last.The RE here refers to REEs such as La, Ce, and the RE addition is meant their summation.
The interpolation of Ca can improve the form of sulfide, and oxide compound and the sulfide of Ca can also promote the ferritic growth of intracrystalline simultaneously, and the Ca content in the steel is advisable with 0.0005～0.004%.When Ca content less than 0.0005% the time; The quantity of the microinclusions that generates and the Ca content in the inclusion will significantly reduce; The ratio that can not satisfy the weight percent content of (Ca+RE)/Al in the inclusion will weaken the effect that microinclusions promotes the growth of intracrystalline ferritic like this more than or equal to 0.3 requirement.If Ca content is greater than 0.004%, the effect of Ca is saturated, has increased vaporization losses and the oxidational losses of Ca simultaneously.
The interpolation of RE also can improve the form of sulfide, and simultaneously RE oxide compound and sulfide can suppress growing up of austenite crystal in the Thermal Cycle process.But, when the content of RE greater than 0.01%, with generating the inclusion of part particle diameter, reduce the impelling strength of mother metal and welded heat affecting zone greater than 5 μ m.
Through analyze finding, when the oxygen level in the molten steel less than 0.001% the time, the quantity not sufficient that will cause fine CaO and/or REO to be mingled with can not be brought into play the effect that promotes that the growth of intracrystalline ferritic, pinning austenite crystal are grown up well.When the oxygen level in the molten steel greater than 0.01% the time, with generating CaO and/or the REO inclusion of part particle diameter greater than 5 μ m, these bigger inclusiones will reduce the impelling strength of mother metal and welded heat affecting zone as the starting point of crackle in the shock test process.Therefore the initial oxygen content in the time of need Ca and/or RE being added accurately is controlled to be 0.001%-0.01%.
The method of initial oxygen position when the invention provides accurate control Ca and/or RE interpolation.When adding SiCa and/or rare earth ferrosilicon alloy, through adding the Fe of trace
2O
3Powder can be realized the accurate control of initial oxygen content when Ca and/or RE add.
The present invention has confirmed the suitable component of inclusion.The components utilising SEM-EDS of inclusion measures, for sample grind with mirror polish after, utilize SEM to observe and analyze for inclusion, the composition of each specimen holder foreign material is a MV of choosing the inclusion analysis result arbitrarily for 10.For the inclusion of particle diameter in the steel more than or equal to 1.0 μ m; (Ca+RE)/ratio of the weight percent content of Al is more than or equal to 0.3 o'clock; Such inclusion can prevent with Al to be the formation of bunch shape inclusion of staple, helps the miniaturization of inclusion.
When the ratio of the weight percent content of Ti/Al in the inclusion more than or equal to 0.15 the time; This is the inclusion formation of staple with Ti; Help promoting separating out of MnS particle, thereby promote the ferritic growth of intracrystalline, improve the large-line energy welding property of Plate Steel on the surface of inclusion.
Because the part of Ca and/or RE combines with S in the molten steel, the sulfide of formation can promote MnS to separate out on its surface, and such MnS particle can promote the ferritic growth of welded heat affecting zone intracrystalline effectively.The present invention finds that the ratio of (the Ca+RE)/Mn content in the steel inclusion also should be 0.25-2.5.When less than 0.25 the time, the quantity that generates Ca and RE sulfide is not enough, can not be effective as the forming core core, and promotion MnS separates out on the surface of Ca and RE inclusion.When greater than 2.5 the time, will significantly reduce with Mn bonded S content, same separating out of MnS will be suppressed.
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 930 ℃, 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, formed thick austenite crystal also can be remaining in the heat-processed, reduced the toughness of mother metal.
Final rolling temperature is less than 930 ℃, and the accumulative total draft is that recrystallize does not take place austenite because under such temperature greater than 30%, 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 rate of cooling during less than 2 ℃/s, strength of parent can not meet the demands with 300～550 ℃ of rate of cooling water-cooled to the final cooling temperatures of 2～30 ℃/s.When rate 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 300 ℃, with the toughness that reduces mother metal.
Beneficial effect of the present invention:
The present invention takes the appropriate ingredients design, and in refining process, takes suitable reductor interpolation order, the addition of control reductor, and through adding Fe
2O
3The mode of powder; Initial oxygen position when accurately controlling Ca and/or RE deoxidation; Can control the Ca of the fine disperse distribution of formation and/or oxide compound and the sulfide inclusion of RE like this, and rationally control for (the Ca+RE)/Al in the inclusion, Ti/Al, (Ca+RE)/Mn ratio.Like this can solidify with phase transition process in form the MnS precipitate at these inclusion spatial inductions, thereby promote the ferritic growth of intracrystalline, improve the large-line energy welding property of Plate Steel.
Embodiment
Below in conjunction with embodiment the present invention is further specified.
In embodiments of the present invention, the alloying constituent in the adjustment molten steel in refining process.And the alloy that adds respective element according to the order of Si, Mn, Al, Ti carries out deoxidation.When guaranteeing alloying constituent, add Fe at last
2O
3Powder, and CaSi alloy and/or rare earth ferrosilicon.The CaSi alloy contains Ca 30%, and surplus is Si, and granularity is 0.1～5mm.Rare earth ferrosilicon contains RE 30.6%, and Si 47.4%, and surplus is Fe, and granularity is 0.1～5mm.
Then strand 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 300～550 ℃ of rate of cooling water-cooled to the final cooling temperatures of 2～30 ℃/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.
Table 1 has been listed (the Ca+RE)/Al in the chemical ingredients, Ti/Nb ratio, inclusion of embodiment and Comparative Examples, Ti/Al with (Ca+RE)/contrast of Mn ratio.Control Al content is less than or equal to 0.02% among the embodiment; The weight percent ratio of Ti/Nb is more than or equal to 1.1 in the steel; For the inclusion of particle diameter in the steel more than or equal to 1.0 μ m; (Ca+RE)/and the ratio of the weight percent content of Al is more than or equal to 0.3, and the ratio of the weight percent content of Ti/Al is more than or equal to 0.15, (Ca+RE)/ratio of Mn weight percent content is 0.25-2.5.
Al content in the Comparative Examples is 0.026% and 0.028%, Ti/Nb ratio in the steel, (the Ca+RE)/Al in the inclusion, Ti/Al, (Ca+RE)/ratio of the weight percent content of Mn in one or multinomially can not satisfy requirement of the present invention.
Table 2 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 1-7 is respectively 184J, 199J, 204J, 162J, 181J, 187J, 181J, 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 present invention takes appropriate ingredients design, confirmed Ti/Nb ratio suitable in the steel.And in steelmaking process, take the suitable reductor interpolation order and the addition of reductor, and add Fe through utilizing
2O
3The mode of powder, the initial oxygen position when accurately controlling Ca and/or RE deoxidation.Can control the Ca of the fine disperse distribution of formation and/or oxide compound and the sulfide inclusion of RE like this, and rationally control for (the Ca+RE)/Al in the inclusion, Ti/Al, (Ca+RE)/Mn weight percent ratio.Such inclusion can solidify with phase transition process in induce and form the MnS precipitate, thereby promote the ferritic generation of intracrystalline, improve 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 (6)
1. large heat input welding steel plates, its chemical component weight per-cent is: C 0.05～0.09%, and Si 0.10～0.30%; Mn 1.3～1.7%, and Ti 0.005～0.03%, and Nb 0.003～0.025%; S:0.001～0.01%, P≤0.015%, N≤0.006%; Al 0.0005～0.02%, Ca0.0005～0.004%, RE≤0.01%; All the other are Fe and inevitable impurity;
Wherein, In the steel in the inclusion of particle diameter more than or equal to 1.0 μ m; (Ca+RE)/and the ratio of Al weight percent content is more than or equal to 0.3, and the ratio of Ti/Al weight percent content is more than or equal to 0.15, (Ca+RE)/ratio of Mn weight percent content is 0.25～2.5.
2. large heat input welding steel plates as claimed in claim 1 is characterized in that, the chemical ingredients of steel also contains more than one elements in Cu≤0.3%, Ni≤0.4% or B≤0.002%, by weight percentage.
3. according to claim 1 or claim 2 large heat input welding steel plates is characterized in that the weight percent ratio of Ti/Nb is more than or equal to 1.1 in the steel.
4. the method for manufacture of a large heat input welding steel plates comprises the steps:
1) smelting, refining and continuous casting
The chemical component weight per-cent of steel is: C 0.05～0.09%, and Si 0.10～0.30%, and Mn 1.3～1.7%; Ti 0.005～0.03%, and Nb 0.003～0.025%, S:0.001～0.01%; P≤0.015%, N≤0.006%, Al 0.0005～0.02%; Ca 0.0005～0.004%, RE≤0.01%; All the other are Fe and inevitable impurity;
Wherein, in the steel liquid deoxidation process, add reductor, reductor kind and interpolation are in proper order: Mn, Si → Al → Ti;
Mode to add SiCa alloy and/or rare earth ferrosilicon adds Ca and/or RE reductor;
And through adding Fe
2O
3Initial oxygen position when powder is controlled Ca and/or RE deoxidation, Fe
2O
3The addition of powder is that to make the oxygen level weight percent in the molten steel be 0.001～0.01%;
In the steel in the inclusion of particle diameter more than or equal to 1.0 μ m; (Ca+RE)/ratio of Al weight percent content is more than or equal to 0.3; The ratio of Ti/Al weight percent content is more than or equal to 0.15, (Ca+RE)/and the ratio of Mn weight percent content is 0.25～2.5;
2) rolling
Strand is heated to 1050～1250 ℃, and the breaking down temperature is higher than 930 ℃, and the accumulative total draft is greater than 30%; Final rolling temperature is less than 930 ℃, and the accumulative total draft is greater than 30%;
3) cooling
With 300～550 ℃ of rate of cooling water-cooled to the final cooling temperatures of 2～30 ℃/s.
5. the method for manufacture of large heat input welding steel plates as claimed in claim 4 is characterized in that, the chemical ingredients of steel also contains more than one elements in Cu≤0.3%, Ni≤0.4% or B≤0.002%, by weight percentage.
6. like the method for manufacture of claim 4 or 5 described large heat input welding steel plates, it is characterized in that the weight percent ratio of Ti/Nb is more than or equal to 1.1 in the steel.
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| CN103695776A (en) * | 2013-12-20 | 2014-04-02 | 宝山钢铁股份有限公司 | Thick steel plate with low carbon equivalent and excellent welding heat affected zone toughness and manufacturing method of same |
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| CN103695776B (en) * | 2013-12-20 | 2016-08-17 | 宝山钢铁股份有限公司 | The steel plate of a kind of low-carbon-equivalent welding heat influence area toughness excellence and manufacture method thereof |
| CN106756541A (en) * | 2016-12-06 | 2017-05-31 | 内蒙古包钢钢联股份有限公司 | 390MPa grades of Large Heat Input Welding offshore platform steel plate and its production method |
| CN109161671A (en) * | 2018-10-10 | 2019-01-08 | 江阴兴澄特种钢铁有限公司 | A kind of Large Heat Input Welding high intensity EH36 steel plate and its manufacturing method |
| CN110029268A (en) * | 2019-03-27 | 2019-07-19 | 江阴兴澄特种钢铁有限公司 | A kind of low-temperature pressure container 09MnNiDR steel plate and manufacturing method for protecting center portion low-temperature flexibility |
| CN112921150A (en) * | 2021-01-29 | 2021-06-08 | 五矿营口中板有限责任公司 | Manufacturing method of aluminum-free low-alloy steel plate suitable for large-line weldable |
| CN114107811A (en) * | 2021-11-17 | 2022-03-01 | 九江萍钢钢铁有限公司 | 700 MPa-grade high heat input resistant welding steel and manufacturing method thereof |
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