CN101153370B - Low alloy high-strength steel plate capable of being welded in large energy input and method of producing the same - Google Patents
Low alloy high-strength steel plate capable of being welded in large energy input and method of producing the same Download PDFInfo
- Publication number
- CN101153370B CN101153370B CN2006100478998A CN200610047899A CN101153370B CN 101153370 B CN101153370 B CN 101153370B CN 2006100478998 A CN2006100478998 A CN 2006100478998A CN 200610047899 A CN200610047899 A CN 200610047899A CN 101153370 B CN101153370 B CN 101153370B
- Authority
- CN
- China
- Prior art keywords
- percent
- steel plate
- rolling
- cooling
- austenite
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Abstract
The invention provides a high strength low alloy steel plate suitable for high heat input welding and is characterized in that the chemical composition (wt percent) of steel comprises 0.04 percent to 0.16 percent of C, 0.10 percent to 0.50 percent of Si, 0.40 percent to 1.8 percent of Mn, 0.020 percent to 0.050 percent of Nb, 0.006 percent to 0.030 percent of Ti, 0.0030 percent to 0.010 percent of N, 0.015 percent to 0.060 percent of Al and the rest, Fe and other inevitable impurities; meanwhile, C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14 is less than or equal to 0.45 percent and the total amount of Ti and the total amount of N are that [Ti percent]T is more than or equal to 2.667[N percent]T-0.004667 percent; moreover, Ti microalloying is adopted to ensure that the Ti/N ratio in the second sort of particle generated ranges between 2.4 and 3.2. The manufacture method of the steel plate adopts austenite recrystallization zone and austenite non-recrystallization zone rolling and forced water cooling after rolling; moreover, when the steel plate is under 50 KJ/cm to 150 KJ/cm high heat input welding, the welding heat affected zone has excellent toughness. The invention has the advantages of simple production process, low cost and wide applicability.
Description
Technical field
The invention belongs to low alloy steel and make the field, but the low-alloy high-strength steel plate and the method for manufacture thereof of the welding of especially a kind of large-line energy.
Background technology
Before the present invention, the public reported of some large-line energies with steel arranged.Patent " unmodified high-toughness low-temp steel for high-energy line welding and method of manufacture thereof " (publication number CN1338528A) and " steel series with high linear energy and low weld crack sensitivity and working method thereof " (publication number CN1396294A) of declaring like Wuhan Iron and Steel Company.These technological common features are to add B, utilize the oxide compound of BN and Ca or Re to suppress the heat affected zone grain growth, improve the heat affected zone performance.But the adding of B often has side effects, and B is easy to gather partially at crystal boundary, causes the serious decline of base metal tenacity.Still there is not at present the good measure of carrying out B.In addition, the oxide compound of Ca, Re control is very difficult, when they when liquid state is separated out, grain growing is unrestricted, does not only have the effect that suppresses grain growth, also can destroy the toughness of mother metal.Therefore, this method is difficult to control aborning.
The patent " welded construction that is used for steel plate and method of manufacture and this steel plate of use of the welded TiN+ZrN of having precipitated phase " (publication number CN1398302A) of Korea S Pu item company application obtains more TiN to stop the grain growth of heat affecting through the content that improves N; Because it is very bad to the continuous casting performance impact of steel that N improves the back; The strand crackle is difficult to avoid; Have to increase and ooze the N operation together, cause production technique and complicacy thereof, production efficiency is low.
Summary of the invention
But the object of the present invention is to provide a kind of low-alloy high-strength steel plate and method of manufacture thereof of large-line energy welding, base metal tenacity reduces, the incompatibility large-line energy requires and produce the unmanageable problem that goes up thereby solve.
The objective of the invention is to realize like this; But a kind of low-alloy high-strength steel plate of large-line energy welding; The chemical ingredients that it is characterized in that steel mainly contains two kinds of schemes; A kind of is (wt%): C:0.04%～0.16%, Si:0.10%～0.50%, Mn:1.30%～1.41%, Nb:0.020%～0.050%, Ti:0.006%～0.030%, N:0.0030%～0.010%, Al:0.015%～0.060%, and surplus is Fe and inevitably is mingled with.Another kind is (wt%): C:0.04%～0.16%, Si:0.10%～0.50%, Mn:1.49%～1.50%, Nb:0.020%～0.050%, Ti:0.006%～0.030%, N:0.0030%～0.010%; Al:0.015%～0.060%; Possibly contain Mo:0.08%～0.40%, Cu in addition :≤0.25%, V:0.02%～0.06%, Ni: one or more of≤0.8%, surplus are Fe and inevitably are mingled with.
For achieving the above object, the present invention also has the following characteristic:
1. adopt the Ti microalloying, make that the Ti/N ratio is between 2.4～3.2 in the second phase particle of generation.
2. make Ti, N total content in the steel satisfy [Ti%]
T>=2.667 [N%] T-0.004667%.Thereby the solid solution in the assurance steel [N%]≤0.002% is improved the toughness of steel plate.
3. control carbon equivalent C
Eq=C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14≤0.45% is to guarantee in the welded heat affecting zone tissue polygonal ferrite more than 15% being arranged.
The present invention adopts the reasons are as follows of mentioned component design:
C is the principal element of decision steel strength, also is the principal element of decision welded heat affecting zone tissue.When C is lower than 0.04%, be difficult to obtain needed intensity; When C is higher than 0.16%, the hardened structure of volume appears in the welded heat affecting zone, and make toughness obtain worsening, and be easy to generate welding crack during high C.C of the present invention is controlled at 0.04%～0.16%.
Si adds as deoxidant element, improves the intensity of steel plate simultaneously, influences the welding property of steel plate.Si is lower than at 0.10% o'clock, and deoxidation effect is poor, and surface of steel plate has been prone to pit and red embroidery; But when Si greater than 0.50% the time, promote microstructure coarsening, and weld hot and cold crack sensitivity and all increase.Si of the present invention is controlled at 0.10%～0.50%.
Atomic radius and the Fe of Mn are close, form substitutional solid solution easily, are the elements of using maximum assurance armor plate strengths, also are the important elements that increases carbon equivalent.When Mn content was lower than 0.4%, intensity reduced, and the deleterious effect of Sization thing strengthens; When Mn content was higher than 1.8%, heat affected zone toughness degenerated.Mn of the present invention is controlled at 0.40%～1.8%.
Ti is the element that the present invention puts forth effort to study.Ti and N are combined into TiN, have the effect that the prevention austenite crystal is grown up and increased the ferritic forming core, can improve the toughness of heat affected zone effectively.The interpolation of Ti can also reduce the solid solution content of N, improves the aging performance of steel.The adding of Ti and N magnitude relation are very big.When the Ti amount is lower than 2.667 [N%]
T-0.004667% o'clock, solid solution N amount was more in the steel, and toughness and aging performance are all lower; When Ti/N is higher than 2.73, the alligatoring of TiN particle, to the beneficial effect weakening of heat affected zone, the Ti of solid solution simultaneously amount increases, the infringement base metal tenacity.Ti/N is between 2.4～3.2 in the control steel, and steel plate and welded heat affecting zone will have higher performance, exceed this scope, and significantly descending will appear in steel plate and welded heat affecting zone aspect of performance.Ti of the present invention is controlled at 0.006%～0.030%.
N is another element of putting forth effort to study of the present invention.N has two kinds of existing waies, and a kind of is solid solution, unfavorable to the mother metal performance, and another kind is to form the fine particle Nization thing that Mass distributes, and welding heat influence area toughness is had the improvement effect.The low then Nization thing quantity not sufficient of N amount is not suitable for the large-line energy welding.N amount height then solid solution N increases, and base metal tenacity and aging performance are bad, and continuously cast bloom is easy to generate crackle.N of the present invention is controlled at 0.003%～0.010%.
Nb can not only improve the recrystallization temperature of the operation of rolling, promotes the refined crystalline strengthening effect, can also form compound Nization thing with Ti, reduces the Ti/N ratio, improves the heat affected zone performance.In the present invention, in order to improve the intensity and the toughness of steel plate through thermo-mechanical rolling, must add the Nb of certain content.Nb measured low, was difficult for performance controlled rolling effect; Nb measures when excessive, in welding process, promotes ferrite side plate to form, and is also unfavorable to toughness.Nb of the present invention is controlled at 0.020%～0.050%.
Al is main deoxidant element.When Al content was low, deoxidizing capacity was not enough, and Ti is oxidized and can not generate useful TiN particle; The Al too high levels forms macrobead easily and is mingled with.Al of the present invention is controlled at 0.015%～0.060%.Be easy to cause copper brittleness, cc billet surface quality problem;
P is an impurity element, increases the fragility of steel, should reduce as far as possible.But it is very high that metallurgy takes off the P cost, and being limited in can the guaranteed performance requirement below 0.015%.
S influences steel flexible principal element.In addition, when S content was high, sulfide can depend on TiN and grow up, and size of particles is increased, and the ability of pinning austenite grain boundary seriously undermines.Good take off the plasticity and toughness that S not only helps to improve steel plate, the size that also helps to control TiN is to suppress growing up of heat affected zone crystal grain.Therefore, satisfy the large-line energy welding requirements and must well take off S.The present invention requires S≤0.010%.
According to steel grade intensity and toughness reguirements, can add among Mo, Ni, V, the Cu one or more.The carbon equivalent but the first three element is significantly increased causes hardenability to increase; Cu can improve the hardening capacity and the resistance to atmospheric corrosion of steel plate, but causes copper brittleness, cc billet surface quality problem easily.Therefore content must limit.The present invention requires that Mo satisfies 0.08%～0.40%, V satisfies 0.02%～0.06%, Cu≤0.25%, Ni≤0.8%.And satisfy C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14≤0.45%.
Plate slab production stage of the present invention should comprise the converter smelting molten steel, and S is taken off in the LF refining, VD or RH vacuum-treat, and forging type can adopt die casting or continuous casting, but is good with the continuous casting mode.
Molten iron pre-desulfurization before the converter smelting, desulfurization slag will be taken off totally.Carry out a deoxidation at converter stage adding Si, Mn.
The LF stove is made white slag, and the degree of depth is taken off S, the target component fine setting.In the deoxidation of LF refining stage secondary.
VD or RH refining, the treatment time was not less than 10 minutes, handled the back at Si-Ca and added Ti-Fe and Nb-Fe, blew Ar gas only 3 minutes, and is even to guarantee composition.Continuous casting superheating temperature≤25 ℃.
The principal character of this smelting technology is at first Mn, Si combined deoxidation, Al secondary deoxidation then, and the finishing operation before continuous casting adds Nb and Ti, and is not oxidized to guarantee Nb and Ti.Thereby in rolling and welding process, bring into play beneficial effect.
Concrete scheme of the present invention also comprises: the rolling method of producing steel plate according to mentioned component.
Steel plate rolling method of the present invention comprises ME such as soaking, roughing, finish rolling, acceleration cooling, aligning.
The present invention does not limit hot steel bloom or cold charge is gone into stove.But hot charging is save energy effectively, should preferentially use.
The Heating temperature of soaking is 1150～1200 ℃.
Rolling technology adopts austenite perfect recrystallization district+two the stage controlled rollings in austenite non-recrystallization district technology after the steel soaking of the present invention.
Roughing adopts the austenite recrystallization district rolling, and temperature range is between 1150～970 ℃, and every time draft is not greater than 10% (containing adjustment dimensional precision passage), and this stage accumulation draft is greater than 50%.
Finish rolling adopts austenite non-recrystallization district rolling, 930～770 ℃ of temperature range controls.Every time draft is greater than 10% (not containing adjustment dimensional precision passage), the cumulative deformation in this stage >=55%.
Rolling the back adopts online laminar flow to quicken cooling.The water temp of going into of steel plate is 740～840 ℃, and the final cooling temperature of steel plate is controlled at 450～650 ℃, and the speed of cooling of steel plate is controlled at 4～20 ℃/s.
The present invention according to the carbon equivalent different mining of steel plate with different process for cooling to obtain required tissue and performances such as intensity, toughness.
When C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14≤0.36%, final cooling temperature is controlled at 500～650 ℃, and the speed of cooling of steel plate is controlled at 4～12 ℃/s, to obtain the tissue that ferritic is the master, keeps steel plate that high toughness is arranged.Be lower than 4 ℃/s like speed of cooling, the ferrite grain size that obtains is more than 20 μ, and toughness is bad, and intensity is also lower.Be higher than 12 ℃/s like speed of cooling, then in tissue, obtain more bainite.
When 0.36%≤C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14≤0.45%, final cooling temperature is controlled at 450～550 ℃, and the speed of cooling of steel plate is controlled at 8～20 ℃/s, to obtain the tissue that bainite is the master, has good combination of strength and toughness.Be lower than 8 ℃/s like speed of cooling, obtain thick bainite and ferritic mixed structure, intensity and toughness are all undesirable.Be higher than 20 ℃/s like speed of cooling, then in tissue, obtain martensite.
Cooling back steel plate carries out on-line straightening, stacking slow cooling then.
The present invention adopts technique scheme can produce following beneficial effect:
1. the steel plate of pressing the present invention's production is when 50～150KJ/cm large-line energy welds, and welding heat influence area toughness is good.
2. chemical composition design is simple, and alloy addition level is few.Compare with conventional steel, under equality strength, by steel grade alloy coefficient (Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14) minimizing about 0.02～0.06% of the present invention's design.Both improve welding property, reduced production cost again.
3. adopt technologies such as austenite perfect recrystallization district+two stage controlled rollings in austenite non-recrystallization district, online laminar flow cooling; Intensity and toughness are improved simultaneously, the steel plate of producing need not be heat-treated under the situation of low-alloy addition can satisfy performance requriements.
4. production technique of the present invention is easy, is fit to produce in batches operation.
Embodiment
Below will be through different embodiment and Comparative Examples the present invention relatively described.These embodiment only are the purposes that is used to explain, the present invention is not limited among these embodiment.
Table 1 is the chemical ingredients of each steel grade in embodiment and the comparative example.Every kind of steel capital is by converter smelting.Table 2 is the smelting condition of each steel grade in embodiment and the comparative example.Table 3 is the rolling technology of each steel grade in embodiment and the comparative example.Table 4 is the conventional mechanical property of each steel grade in embodiment and the comparative example.Table 5 is the welding property of each steel grade in embodiment and the comparative example.
Visible by table 1～table 5, on same strength level, the steel plate that utilizes the present invention to produce has lower carbon equivalent, and heat affected zone toughness is also far above the contrast steel plate under the large-line energy welding conditions.
Table 2, the smelting condition of each steel grade in embodiment and the comparative example.(Wt，％)
| Steel grade | Refining unit | The deoxidation order | Nb adds the place | Ti adds the place |
| Embodiment 1 | LF+VD | Mn、Si、Al | VD | VD |
| Comparative Examples 1 | LF | Mn、Si、Al | LF | LF |
| Embodiment 2 | LF+VD | Mn、Si、Al | VD | VD |
| Comparative Examples 2 | LF+VD | Mn、Si、Al | LF | LF |
| Embodiment 3 | LF+RH | Mn、Si、Al | RH | RH |
| Comparative Examples 3 | RH+LF | Mn、Si、Al | RH | RH |
| Embodiment 4 | LF+VD | Mn、Si、Al | VD | VD |
| Comparative Examples 4 | LF+VD | Mn、Si、Al | LF | LF |
Claims (4)
1. but the low-alloy high-strength steel plate of large-line energy welding; The chemical component weight per-cent that it is characterized in that steel is: C:0.04%～0.16%, Si:0.10%～0.50%, Mn:1.30%～1.41%, Nb:0.020%～0.050%, Ti:0.006%～0.030%, N:0.0030%～0.010%, Al:0.015%～0.060%; Surplus is Fe and inevitably is mingled with, also should satisfy C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14≤0.45% and total Ti content and total N content and meet [Ti%]
T>=2.667 [N%]
T-0.004667%, and adopt the Ti microalloying, make that the Ti/N ratio is 2.4～3.2 in the second phase particle of generation.
2. but the low-alloy high-strength steel plate of large-line energy welding; The chemical component weight per-cent that it is characterized in that steel is: C:0.04%～0.16%, Si:0.10%～0.50%, Mn:1.49%～1.50%, Nb:0.020%～0.050%, Ti:0.006%～0.030%, N:0.0030%～0.010%, Al:0.015%～0.060%; Also contain Mo:0.08%～0.40%, Cu :≤0.25%, V:0.02%～0.06%, Ni: one or more of≤0.8%; Surplus is Fe and inevitably is mingled with, also should satisfy C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14≤0.45% and total Ti content and total N content and meet [Ti%]
T>=2.667 [N%]
T-0.004667%, and adopt the Ti microalloying, make that the Ti/N ratio is 2.4～3.2 in the second phase particle of generation.
3. but the method for manufacture of the low-alloy high-strength steel plate of the described large-line energy welding of a claim 1; Adopt austenite recrystallization district and austenite non-recrystallization district two stage rolling after it is characterized in that to contain the steel billet soaking of above-mentioned chemical ingredients, carry out Forced water cooling after rolling; Be specially: billet heating temperature is 1176～1200 ℃; Roughing adopts the austenite recrystallization district rolling, and temperature range is between 1150～970 ℃, and every time draft is greater than 10%, and this stage accumulation draft is greater than 50%; Finish rolling adopts austenite non-recrystallization district rolling, 930～770 ℃ of temperature range controls, and every time draft is greater than 10%, the cumulative deformation in this stage >=55%; Roll the back and adopt online laminar flow to quicken cooling, the water temp of going into of steel plate is 740～840 ℃, and the final cooling temperature of steel plate is controlled at 450～650 ℃, and the speed of cooling of steel plate is controlled at 4～20 ℃/s.
4. but the method for manufacture of the low-alloy high-strength steel plate of the described large-line energy welding of a claim 2; Adopt austenite recrystallization district and austenite non-recrystallization district two stage rolling after it is characterized in that to contain the steel billet soaking of above-mentioned chemical ingredients, carry out Forced water cooling after rolling; Be specially: billet heating temperature is 1179～1200 ℃; Roughing adopts the austenite recrystallization district rolling, and temperature range is between 1150～970 ℃, and every time draft is greater than 10%, and this stage accumulation draft is greater than 50%; Finish rolling adopts austenite non-recrystallization district rolling, 930～770 ℃ of temperature range controls, and every time draft is greater than 10%, the cumulative deformation in this stage >=55%; Roll the back and adopt online laminar flow to quicken cooling, the water temp of going into of steel plate is 740～840 ℃, and the final cooling temperature of steel plate is controlled at 450～650 ℃, and the speed of cooling of steel plate is controlled at 4～20 ℃/s.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2006100478998A CN101153370B (en) | 2006-09-27 | 2006-09-27 | Low alloy high-strength steel plate capable of being welded in large energy input and method of producing the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2006100478998A CN101153370B (en) | 2006-09-27 | 2006-09-27 | Low alloy high-strength steel plate capable of being welded in large energy input and method of producing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN101153370A CN101153370A (en) | 2008-04-02 |
| CN101153370B true CN101153370B (en) | 2012-06-13 |
Family
ID=39255253
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN2006100478998A Active CN101153370B (en) | 2006-09-27 | 2006-09-27 | Low alloy high-strength steel plate capable of being welded in large energy input and method of producing the same |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN101153370B (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107287508A (en) * | 2016-04-04 | 2017-10-24 | 鞍钢股份有限公司 | A kind of production method of the 40kg grades of Large Heat Input Welding deck of boat |
Families Citing this family (25)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101660105B (en) * | 2008-08-26 | 2011-05-11 | 宝山钢铁股份有限公司 | High-strength extra-thick quenched and tempered steel plate with good obdurability matching and manufacturing method thereof |
| CN101906585B (en) * | 2009-06-08 | 2014-04-02 | 鞍钢股份有限公司 | High-performance building structure refractory steel plates and manufacturing method thereof |
| CN102022086B (en) * | 2009-09-15 | 2013-09-04 | 鞍钢股份有限公司 | Manufacturing method of economical seamless oil well pipe for expansion pipe |
| CN102102162A (en) * | 2009-12-22 | 2011-06-22 | 鞍钢股份有限公司 | Steel plate with low M-A content in high heat input welding heat affected zone |
| KR101360737B1 (en) * | 2009-12-28 | 2014-02-07 | 주식회사 포스코 | High strength steel plate having excellent resistance to brittle crack initiation and method for manufacturing the same |
| CN101812639A (en) * | 2010-04-20 | 2010-08-25 | 马鞍山钢铁股份有限公司 | Steel used for welding hull with high strength and high input energy and production method thereof |
| CN102251173B (en) * | 2010-05-17 | 2014-04-30 | 宝山钢铁股份有限公司 | High-strength and high-toughness steel plate for low-cost and high linear energy welding |
| CN102373371B (en) * | 2010-08-25 | 2013-10-30 | 宝山钢铁股份有限公司 | Method for raising large heat input weldability of thick steel plate |
| CN102400049B (en) * | 2010-09-07 | 2014-03-12 | 鞍钢股份有限公司 | 490-grade fireproof steel plate for building structure and manufacturing method thereof |
| CN102400053B (en) * | 2010-09-07 | 2014-03-12 | 鞍钢股份有限公司 | Steel plate for building structure with yield strength of 460 MPa, and manufacturing method thereof |
| CN102121060B (en) * | 2011-02-18 | 2013-02-13 | 济钢集团有限公司 | Method for improving strength and toughness of high-strength steel for coal machine by utilizing ultra-fast cooling and steel plate self-tempering technologies |
| CN104066858B (en) * | 2012-01-18 | 2015-11-25 | 杰富意钢铁株式会社 | The manufacture method of taper plate |
| CN103361551A (en) * | 2012-03-30 | 2013-10-23 | 鞍钢股份有限公司 | V-N microalloying based high toughness ship board and preparation method thereof |
| CN103725980A (en) * | 2013-10-26 | 2014-04-16 | 溧阳市浙大产学研服务中心有限公司 | High-performance magnetic control connecting piece |
| CN103938092B (en) * | 2014-03-24 | 2016-05-11 | 济钢集团有限公司 | A kind of high-fatigue strength thermoforming heavy truck axle housing steel plate |
| CN104328339A (en) * | 2014-11-04 | 2015-02-04 | 钢铁研究总院 | Vanadium nitrogen composite micro-alloy high-strength pressure vessel steel plate and preparation method |
| CN104907335B (en) * | 2015-06-25 | 2017-05-10 | 江阴兴澄特种钢铁有限公司 | Supercooling austenite rolling method suitable for carbon-manganese medium steel plate |
| CN106086650B (en) * | 2016-07-25 | 2018-05-01 | 江阴兴澄特种钢铁有限公司 | It is a kind of can Large Heat Input Welding polar region ship plate and preparation method thereof |
| JP6771429B2 (en) * | 2016-08-29 | 2020-10-21 | 株式会社神戸製鋼所 | Thick steel plate and its manufacturing method |
| CN108070779A (en) * | 2016-11-13 | 2018-05-25 | 广东韶钢松山股份有限公司 | A kind of solderable fine grain, high strength degree structural steel and iron and its production method |
| CN108165893A (en) * | 2017-12-26 | 2018-06-15 | 苏州贝尔纳德铁路设备有限公司 | A kind of internal combustion changes windlass low-alloy high-strength steel plate and its production method |
| CN111500937B (en) * | 2020-05-28 | 2021-10-22 | 鞍钢股份有限公司 | 460 MPa-level bridge channel steel and production method thereof |
| CN111500938B (en) * | 2020-05-28 | 2021-11-12 | 鞍钢股份有限公司 | Channel steel with yield strength of 420MPa for bridge and production method |
| CN112080698A (en) * | 2020-09-09 | 2020-12-15 | 鞍钢股份有限公司 | FCB (flux cored wire) high heat input weldable structural steel and manufacturing method and welding process thereof |
| CN112458365A (en) * | 2020-11-06 | 2021-03-09 | 新余钢铁股份有限公司 | Vanadium-free normalized high-toughness thick ship plate with thickness of more than or equal to 60mm and production method thereof |
-
2006
- 2006-09-27 CN CN2006100478998A patent/CN101153370B/en active Active
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107287508A (en) * | 2016-04-04 | 2017-10-24 | 鞍钢股份有限公司 | A kind of production method of the 40kg grades of Large Heat Input Welding deck of boat |
Also Published As
| Publication number | Publication date |
|---|---|
| CN101153370A (en) | 2008-04-02 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101153370B (en) | Low alloy high-strength steel plate capable of being welded in large energy input and method of producing the same | |
| CN101775539B (en) | High-flexibility wear-resistant steel plate and manufacturing method thereof | |
| CN103146997A (en) | Low-alloy high-toughness wear resistant steel plate and manufacturing method thereof | |
| CN109385576A (en) | A kind of inexpensive X65 pipe line steel and its manufacturing method based on magnesium processing | |
| CN106939391A (en) | A kind of Ca microalloyings easy-cutting high strength fractured connecting rod steel and manufacture method | |
| CN107964624A (en) | A kind of yield strength 500MPa level structure steel and preparation method thereof | |
| CN102206787B (en) | Low-roll-force gas-transmission pipeline steel and production method thereof | |
| CN107475624A (en) | Titaniferous think gauge weathering steel and its production method | |
| CN109881089B (en) | High-strength wear-resistant steel and preparation method thereof | |
| CN102102162A (en) | Steel plate with low M-A content in high heat input welding heat affected zone | |
| CN110629114A (en) | Low-cost high-strength high-toughness bridge steel and preparation method thereof | |
| CN105112782A (en) | Low-temperature ferrite LT-FH40 steel plate applied to hot-rolled ships and production method thereof | |
| CN107675086B (en) | A kind of automobile-used hot-rolled structural steel of 800MPa grades of engineering and its production method | |
| CN104264072A (en) | 600HB (Brinell hardness) grade wear-resistant steel plate and preparation method thereof | |
| CN102345066A (en) | Steel used for pressure container and preparation method thereof | |
| CN100463994C (en) | Nb-Ti microalloying steel suitable for large line energy welding and smelting method therefor | |
| CN102953016B (en) | A kind of 650HB grade wear-resisting steel plate and manufacture method thereof | |
| CN106435360A (en) | High-strength, high-toughness, corrosion-resistant and weather-resistant steel plate and manufacturing method thereof | |
| CN106811684A (en) | Yield strength 750Mpa grades of container hot rolled steel plate and its manufacture method | |
| CN113846260A (en) | Production method of high-strength steel plate for engineering machinery | |
| CN102418047B (en) | Non-quenched and tempered fatigue-resistant steel plate and manufacturing method thereof | |
| CN112877591A (en) | High-strength and high-toughness steel for hardware tool and chain and manufacturing method thereof | |
| CN108034897B (en) | Ultra-thick plate produced under low compression ratio condition and production method thereof | |
| CN103667921A (en) | Thick steel plate with high strength and toughness as well as uniform performance in thickness direction and production method of thick steel plate | |
| CN107034413B (en) | The wear-resisting strip of low quenching degree and its manufacturing method |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant |