CN103103441B - Pressure container steel with high toughness at -140 DEG C and production method thereof - Google Patents
Pressure container steel with high toughness at -140 DEG C and production method thereof Download PDFInfo
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Abstract
The invention relates to pressure container steel with high toughness at -140 DEG C. The pressure container steel comprises the following components by weight: less than or equal to 0.05 of C, less than or equal to 0.05 of Si, 0.50-1.00 of Mn, less than or equal to 0.006 of P, less than or equal to 0.003 of S, 0.015-0.050 of Alt, 4.50-5.30 of Ni, 0.02-0.05 of Nb, 0.008-0.025 of Ti, less than or equal to 0.004 of N and one or more of less than or equal to 0.50 of Cr, less than or equal to 0.50 of Mo, less than or equal to 0.30 of Cu and less than or equal to 0.005 of Ca. A process of the pressure container steel comprises the following steps: smelting and continuously casting to form a blank; heating a casting blank; rough rolling at a first stage; rough rolling at a second stage after cooling for the first time; finish rolling after cooling for the second time; and carrying out heat treatment according to the thickness of a steel plate for later use. When the pressure container steel is at -140 DEG C, KV2 is not less than 100J, a transverse crack thickness rate CTR is less than or equal to 3%, a transverse crack length rate CLR is less than or equal to 10%, a transverse crack sensitivity rate is less than or equal to 1.5%, the content of Ni is low, and the welding performance is excellent.
Description
Technical field
The present invention relates to container steel alloy and production method thereof, belong to a kind of low-temperature pressure vessel steel and production method thereof particularly, further for being suitable for pressure vessel steel and the production method thereof of ﹣ 140 DEG C.
Background technology
Before the present invention proposes, although some research work of existing Ni system low-temperature steel, its thought channel is the mode that the content of the Ni added along with the reduction of temperature will increase thereupon, and this causes production cost higher.As, through retrieval, Japanese documentation JP60059032 discloses " a kind of excellent low temperature toughness and low yield strength ratio high-nickel steel plate and manufacture method " thereof, and its Ingredient percent is C≤0.03, Si:0.02 ~ 0.22, Mn:0.05 ~ 0.47, P≤0.005, S≤0.005, Ni:7.5 ~ 12.0, Al:0.01 ~ 0.10, can add C, Mn or Nb(0.005 ~ 0.03 when needing) or V(0.005 ~ 0.03) etc. more than one elements, all the other are Fe and inevitable impurity ".Although the steel grade disclosed in the document can meet i.e.-160 DEG C of environment for use requirements of extremely low temperature, which are added the Ni of 7.5 ~ 12.0, cause production cost high, application is restricted.
Japanese Patent JP7173534 " a kind of containing Ni high tenacity low-temperature steel plate and manufacture method thereof ", its Ingredient percent is C:0.01 ~ 0.12, Si:0.10 ~ 0.30, Mn:0.1 ~ 1.0, P≤0.010, S≤0.005, Al:0.005 ~ 0.050, Ni:7.5 ~ 10.0, all the other are Fe and inevitable impurity.Its not enough nickel content existed is still higher, namely 7.5 ~ 10.0%.
Be also the document of 201110331478.9 just like Chinese patent number of patent application, disclose " a kind of high-tenacity-130 DEG C low-temperature steel and manufacture method thereof ", involved steel has following ingredients and mass percent is C≤0.12, Si:0.10 ~ 0.35, Mn:0.30 ~ 1.00, P≤0.015, S≤0.005, Ni:4.70 ~ 5.30, Al:0.005 ~ 0.10, in addition containing Nb≤0.040, V≤0.06, Cr≤0.25, Mo≤0.50, Zr≤0.050, one or more in RE≤0.020, all the other are Fe and inevitable impurity.In the document, Ni is content 4.70 ~ 5.30%, and its Japanese Patent is lower relatively, but its adaptive temperature only has-130 DEG C, can not be applicable to the making of the pressurized vessel under lower temperature environment.
Summary of the invention
Especially Ni content is higher to the object of the invention is to overcome the alloy of existing low-temperature (low temperature) vessel steel steel grade, temperature with containing Ni deficiency inversely, KV at providing a kind of-140 DEG C
2be not less than 100J, transverse crack thickness rate CTR≤3%, transverse crack length rate CLR≤10%, transverse crack Sensitivity rate CSR≤1.5%, Ni content is low, pressure vessel steel and the production method thereof of what welding property was excellent be suitable for ﹣ 140 DEG C.
Realize the measure of above-mentioned purpose:
Have a steels for pressure vessel use for high tenacity at ﹣ 140 DEG C, its component and weight percent content are: C≤0.05, Si≤0.05, Mn:0.50 ~ 1.00, P≤0.006, S≤0.003, Alt:0.015 ~ 0.050, Ni:4.50 ~ 5.30, Nb:0.02 ~ 0.05, Ti:0.008 ~ 0.025, N≤0.004, in addition containing Cr≤0.50, Mo≤0.50, Cu≤0.30, Ca≤0.005, in one or more than one, surplus is Fe and is inevitably mingled with.
Have a steels for pressure vessel use for high tenacity at ﹣ 140 DEG C, its component and weight percent content are: C≤0.03, Si≤0.05, Mn:0.60 ~ 1.00, P≤0.006, S≤0.003, Alt:0.015 ~ 0.050, Ni:4.50 ~ 5.00, Nb:0.02 ~ 0.05, Ti:0.008 ~ 0.025,, N≤0.004, Cu:0.10 ~ 0.30, Ca:0.002 ~ 0.005, surplus is Fe and is inevitably mingled with.
Have a steels for pressure vessel use for high tenacity at ﹣ 140 DEG C, its component and weight percent content are: C:0.03 ~ 0.05, Si≤0.05, Mn:0.50 ~ 0.80, P≤0.006, S≤0.003, Alt:0.015 ~ 0.050, Ni:5.00 ~ 5.30, Nb:0.02 ~ 0.05, Ti:0.008 ~ 0.025, N≤0.004, Cr:0.10 ~ 0.40, Mo:0.20 ~ 0.40, Ca:0.002 ~ 0.005, surplus is Fe and is inevitably mingled with.
There is at producing a kind of ﹣ 140 DEG C the method for the steels for pressure vessel use of high tenacity, the steps include:
1) smelt also continuous casting and become base: in LF stove, carry out Ca process, in control molten steel, Ca is within target; Control RH vacuum processing time is not less than 20 minutes;
2) to strand heating, control Heating temperature at 1200 ~ 1300 DEG C, control heating rate at 9 ~ 12 minutes/centimetre;
3) carry out the first rough rolling step, the start rolling temperature controlling this stage is not less than 1100 DEG C;
4) through for the first time after temperature, at start rolling temperature is 1000 DEG C ~ 1050 DEG C, subordinate phase roughing is carried out;
5) through for the second time after temperature, at start rolling temperature is 930 DEG C ~ 960 DEG C, carry out finish rolling, controlling finishing temperature is 760 ~ 820 DEG C;
6) heat-treat according to steel plate thickness:
When steel plate thickness is at 10 ~ 20 millimeters, the mode adopting normalizing to add quick cooling+tempering is carried out, and normalizing temperature is 800 ~ 900 DEG C, and the normalizing time is (minute): t+30, and tempering temperature is 600 ~ 680 DEG C, and tempering time is (minute): t+50; In formula: t is the thickness of steel plate, unit is millimeter; When cooling fast, red temperature controls at 400 ~ 600 DEG C;
When steel plate thickness is being greater than 20 to when being no more than 40 millimeters, adopt the mode of quenching+tempering to carry out, quenching temperature is 800 ~ 900 DEG C, and the cool time is (minute): t+30, and tempering temperature is 600 ~ 680 DEG C, and tempering time is (minute): t+50;
In formula: t is the thickness of steel plate, unit is millimeter;
When steel plate thickness is being greater than 40 to when being no more than 60 millimeters, adopt the mode of two quenching+temperings to carry out, quenching temperature is 800 ~ 900 DEG C for the first time, and the cool time is (minute): t+30; Second time quenching temperature is 750 ~ 850 DEG C, and the cool time is (minute): t+30; Tempering temperature is 600 ~ 680 DEG C, and tempering time is (minute): t+50;
In formula: t is the thickness of steel plate, unit is millimeter;
7) stand-by.
Composition and the main production setting reason of steel of the present invention are below described in detail in detail:
Simultaneously the maximum difficult point of this steel to guarantee having excellent toughness (-140 DEG C), welding property and resistance against hydrogen cracking (HIC) performance.Therefore, strictly to control the purity of molten steel during steel-making, prevent P, S content on the impact of this steel anti-H 2 S stress corrosion performance.The design mix of Mn, Nb, Cu, Ti, Ni ensure that the intensity of steel, toughness and welding property, wherein Ni alloy is mainly used to the low-temperature flexibility improving steel, Ti alloy can refinement Plate Welding heat affected zone tissue, and improve toughness levels, Cu, Mo can improve the stability after steel plate SR.Generally speaking, adopt on the combined microalloying of Ni, Ti, Cu, Cr, Mo and other elements, the feature of each element be given full play to.P≤0.008% is set, S≤0.003%, N≤0.004%, mainly considers that these elements are comparatively large to this steel low-temperature flexibility and resistance against hydrogen cracking (HIC) performance impact, will strictly limit its content.
C:C improves the most effective element of steel strength, along with the increase of C content, and Fe in steel
3c increases, and hardenability also increases, and the tensile strength of steel and yield strength improve.But, increase C content in steel, the unit elongation of steel and impact toughness decreased, especially larger on low-temperature flexibility impact.Therefore, consider low-temperature flexibility and the welding property requirement of steel, adopt low C to design and the C content of steel of the present invention should be controlled within 0.05%.
The avidity of Si:Si and carbon is very weak, not carburet in steel, but can dissolve in ferrite, produces solution strengthening effect, ferritic intensity and hardness are improved, but plasticity and toughness declines to some extent.Consider that this steel mainly requires higher to steel plate low-temperature flexibility, low Si therefore should be selected to design, and the Si content of steel of the present invention controls within 0.05%.
Mn:Mn improves the yield strength of steel and the one of the chief elements of tensile strength, can add appropriate Mn to improve armor plate strength, and cost is lower at low-carbon (LC) steel grade, therefore general interpolation more than 0.40%.But Mn element is a kind of element of easy segregation, when line of segragation Mn, C content reach certain proportion, produce at steel and can produce martensitic phase in welding process, this is met and shows very high hardness, has considerable influence to steel plate low-temperature flexibility and resistance against hydrogen cracking performance.Meanwhile, Mn content Gao Shihui causes steel plate superheated susceptivity to increase, and when slightly overheated, crystal grain alligatoring will occur, larger on low-temperature flexibility impact.Therefore, consider Mn content is limited in 0.50% ~ 1.00% scope.
Al:Al is the main deoxidant element in steel, and the Al of certain content can also the crystal grain of refinement steel plate, improves intensity and the toughness of steel plate.But when Al content is higher, easily cause being mingled with in steel increasing, unfavorable to the toughness of steel, hardenability and the toughness of steel can be reduced simultaneously, reduce the resistance against hydrogen cracking performance of steel.Therefore Alt content in steel of the present invention is controlled within 0.015% ~ 0.050%.
Ni:Ni can melt with any ratio mutually with iron, is improved the low-temperature flexibility of steel by fining ferrite grains, obviously can reduce the low temperature ductile-brittle transition temperature of steel plate.From domestic and international similar steel grade, the Ni content of 4.50% is the most basic requirement.Lower than this numerical value, the use temperature of steel does not reach-120 DEG C of requirements, but Ni content is too high will increase smelting difficulty, significantly improves production cost.Therefore, Ni content is set within 4.50% ~ 5.30% by steel of the present invention.
Ti: Ti is a kind of strong carbide and nitride forming element, TiN, Ti(CN of formation) etc. particle highly stable, effectively can stop grain growth when forming core, therefore, it is possible to crystal grain thinning, improve the intensity of steel plate and toughness.But Ti is obvious not as good as Nb to intensity contribution, the carbide that too much Ti is formed simultaneously can reduce steel plate low-temperature flexibility.The effect of steel plate Ti when welding is also obvious, can effective refinement welded heat affecting zone tissue.Consider the requirement of steel plate low-temperature flexibility and the impact on welding property, the content time control of design Ti is built in 0.008% ~ 0.025%.
Cu: Cu mainly plays precipitation strength effect in steel, useful to the low-temperature flexibility of steel after stress-removal thermal treatment, can improve the fatigue crack extended capability that can also improve steel in addition.But when Cu too high levels, easily there is map cracking when rolling in steel.Consider the impact of Cu on steel plate comprehensive mechanical property and corrosion resistance, Cu content is controlled within 0.30%.
Cr:Cr is element conventional in hydrogen sulfide corrosion resistant steel, can obtain stable tissue, can improve steel anti-hydrogen embrittlement ability and anti-H 2 S stress corrosion performance after under thermal treatment.Meanwhile, consider cost of alloy and service requirements, Cr content is controlled 0.50%.
Mo:Mo is the element effectively improving steel plate temper resistance, can improve armor plate strength and resistance against hydrogen cracking performance.If addition is too high, steel plate low-temperature flexibility can be caused to decline, therefore, steel Mo content of the present invention controls within 0.50%.
Nb:Nb is a kind of carbide, in steel, form NbC, Nb(CN) etc. Second Phase Particles, hinder the growing up of austenite crystal, crystal grain thinning, improve intensity and the low-temperature flexibility of steel plate.The operative temperature of Nb element is higher than Ti and V, is also greater than Ti and V to the contribution of armor plate strength, easily produces intergranular crack during its too high levels.Therefore, consider Nb content of the present invention is controlled within 0.040%.
Ca:Ca is the element that steel increases when carrying out Ca process, and when its content is not high, element itself has no significant effect plate property, but after Ca process, steel inclusion appearance changes, size reduces, and Oxygen potential improves, and is conducive to the hydrogen sulfide corrosion resistance energy of steel.But in steel, impurity element increases after considering Ca process, therefore, add-on is unsuitable excessive, and Ca content after process controls within 0.005% by this steel.
The impact of impurity element and gas antagonism H 2 S stress corrosion Steel Properties
Low-temperature pressure vessel steel will guarantee the use in low temperature environment.Impurity element in steel and gas on the low-temperature flexibility impact of steel plate comparatively greatly, therefore will reduce the content of P, S, N as much as possible.
P:P in steel except formed can cause steel red crisp (hot-short) and plasticity reduction meltable eutectic inclusion except, also process is reconfigured to hydrogen atom and play restraining effect, make steel increase hydrogen effect to increase, thus improve the fragility of steel, reduce low-temperature flexibility level and resistance against hydrogen cracking performance.Therefore, P should be controlled within 0.006% for this steel.
Steel plate then can be made to have anisotropy for S:S too high levels and toughness reduces, and the stability of steel is sharply worsened.Therefore, S should be controlled within 0.003% for this steel.
In addition, this steel should reduce gas content in steel as far as possible, reduces the segregation of steel.Meanwhile, in order to reduce the influence of time effect of steel, the content of N is controlled within 0.004%.
The reason of production technique setting
(1) process for making
Why the present invention carries out Ca process and vacuum processing time is not less than 18 minutes at LF stove: the object of carrying out Ca process at LF stove is exactly to carry out sex change to inclusion, and effectively reduce inclusion size, change the shape of inclusion, be conducive to the hydrogen sulfide corrosion resistance energy of steel; Adopting in vacuum-treat and be not less than 20 minutes, is to reduce impurity and gas content in steel.
(2) steel rolling process
The present invention takes two-phase control rolling mode when carrying out roughing rolling, and namely first rough rolling step → first time treated that temperature → the second rough rolling step → second time treated temperature, and this kind of rolling technology is highly profitable to the low-temperature flexibility improving steel plate.
During roughing, also will according to finished steel plate thickness, the thickness of intermediate blank at the end of controlling rough rolling step rolling.First time treats temperature, is in order to ensure avoiding mixed crystal temperature range; Second time treats temperature, is to avoid austenite fraction recrystallization zone temperature, finish rolling is carried out at austenite Unhydrated cement.And after making finish rolling finish to gauge, generation is replied and polygonization by deformation dislocation, thus thinning microstructure, improve the low-temperature flexibility of steel plate, can be also useful to the hydrogen sulfide corrosion resistance of steel.
(3) processing, thermal treatment process
Because this steel will life-time service at low ambient temperatures, and require higher to the resistance against hydrogen cracking performance of steel, so for the feature of this steel, consider different steel plate thickness simultaneously, and adopt different heat treating regimes: when steel plate thickness is at 10 ~ 20 millimeters, the mode adopting normalizing to add quick cooling+tempering is carried out, thus the metallographic structure obtained is a kind of more stable ferrite+pearlitic structure.
When steel plate thickness is being greater than 20 to when being no more than 40 millimeters, adopt the heat treatment mode of quenching+tempering, thus the metallographic structure obtained is a kind of more stable ferrite+bainite structure.
When steel plate thickness is being greater than 40 to when being no more than 60 millimeters, adopt the heat treatment mode of two quenching+temperings, thus the metallographic structure obtained is a kind of more stable ferrite+bainite structure.
The present invention compared with prior art, KV at-140 DEG C
2be not less than 100J, transverse crack thickness rate CTR≤3%, transverse crack length rate CLR≤10%, transverse crack Sensitivity rate CSR≤1.5%, Ni content is low, and welding property is excellent, and Ni consumption is few, advantage of lower cost, closer to large production.
Embodiment
Below the present invention is described in detail:
Table 1 is the value list of various embodiments of the present invention and comparative example;
Table 2 is the main technologic parameters list of various embodiments of the present invention and comparative example;
Table 3 is the embodiment of the present invention and the thermal treatment process list contrasting steel grade;
Table 4 is the embodiment of the present invention and the mechanics assay contrasting steel grade;
Table 5 is the embodiment of the present invention and the hydrogen sulfide corrosion resistant assay contrasting steel grade.
Various embodiments of the present invention are produced according to following steps:
Its step:
1) smelt also continuous casting and become base: in LF stove, carry out Ca process, in control molten steel, Ca is within target; Control RH vacuum processing time is not less than 20 minutes;
2) to strand heating, control Heating temperature at 1200 ~ 1300 DEG C, control heating rate at 9 ~ 12 minutes/centimetre;
3) carry out the first rough rolling step, the start rolling temperature controlling this stage is not less than 1100 DEG C;
4) through for the first time after temperature, at start rolling temperature is 1000 DEG C ~ 1050 DEG C, subordinate phase roughing is carried out;
5) through for the second time after temperature, at start rolling temperature is 930 DEG C ~ 960 DEG C, carry out finish rolling, controlling finishing temperature is 760 ~ 820 DEG C;
6) heat-treat according to steel plate thickness:
When steel plate thickness is at 10 ~ 20 millimeters, the mode adopting normalizing to add quick cooling+tempering is carried out, and normalizing temperature is 800 ~ 900 DEG C, and the normalizing time is (minute): t+30, and tempering temperature is 600 ~ 680 DEG C, and tempering time is (minute): t+50; In formula: t is the thickness of steel plate, unit is millimeter; When cooling fast, red temperature controls at 400 ~ 600 DEG C;
When steel plate thickness is being greater than 20 to when being no more than 40 millimeters, adopt the mode of quenching+tempering to carry out, quenching temperature is 800 ~ 900 DEG C, and the cool time is (minute): t+30, and tempering temperature is 600 ~ 680 DEG C, and tempering time is (minute): t+50;
In formula: t is the thickness of steel plate, unit is millimeter;
When steel plate thickness is being greater than 40 to when being no more than 60 millimeters, adopt the mode of two quenching+temperings to carry out, quenching temperature is 800 ~ 900 DEG C for the first time, and the cool time is (minute): t+30; Second time quenching temperature is 750 ~ 850 DEG C, and the cool time is (minute): t+30; Tempering temperature is 600 ~ 680 DEG C, and tempering time is (minute): t+50;
In formula: t is the thickness of steel plate, unit is millimeter;
7) stand-by.
Table 1 embodiment of the present invention and contrast steel grade chemical composition (wt%)
Table 2 embodiment of the present invention and the main processes contrasting steel grade
Table 3 embodiment of the present invention and the heat treatment process contrasting steel grade
Table 4 embodiment of the present invention and the mechanics assay contrasting steel grade
Table 5 embodiment of the present invention and the hydrogen sulfide corrosion resistant assay contrasting steel grade
As can be seen from table 4 ~ 5, steel grade steel of the present invention is pure, has good low-temperature flexibility, resistance against hydrogen cracking performance, the petrochemical industry used under can be used for manufacturing-100 DEG C ~-140 DEG C low temperature environments and fertilizer industry pressure vessel and equipment.
Above-described embodiment is only the best and exemplifies, and is not the restriction to embodiments of the present invention.
Claims (4)
1. there is at a ﹣ 140 DEG C the steels for pressure vessel use of high tenacity, its component and weight percent content are: C≤0.028, Si≤0.05, Mn:0.50 ~ 1.00, P≤0.006, S≤0.003, Alt:0.015 ~ 0.023, Ni:4.50 ~ 4.67, Nb:0.047 ~ 0.05, Ti:0.008 ~ 0.025, N≤0.004, in addition containing Cr:0.36 ~ 0.5 or≤0.11, Mo:0.28 ~ 0. 5 or≤0.21, Cu≤0.30, Ca≤0.005, in one or more than one, surplus is Fe and is inevitably mingled with.
2. have a steels for pressure vessel use for high tenacity at ﹣ 140 DEG C, its component and weight percent content are: C≤0.028, Si≤0.05, Mn:0.60 ~ 1.00, P≤0.006, S≤0.003, Alt:0.015 ~ 0.023, Ni:4.50 ~ 4.67, Nb:0.047 ~ 0.05, Ti:0.008 ~ 0.025, N≤0.004, Cu:0.10 ~ 0.30, Ca:0.002 ~ 0.005, surplus is Fe and is inevitably mingled with.
3. have a steels for pressure vessel use for high tenacity at ﹣ 140 DEG C, its component and weight percent content are: C:0.03 ~ 0.05, Si≤0.05, Mn:0.50 ~ 0.80, P≤0.006, S≤0.003, Alt:0.015 ~ 0.023, Ni:4.50 ~ 4.67, Nb:0.047 ~ 0.05, Ti:0.008 ~ 0.025, N≤0.004, Cr:0.36 ~ 0.40, Mo:0.28 ~ 0.40, Ca:0.002 ~ 0.005, surplus is Fe and is inevitably mingled with.
4. there is at producing a kind of ﹣ 140 DEG C as described in claim 1 or 2 or 3 method of the steels for pressure vessel use of high tenacity, the steps include:
1) smelt also continuous casting and become base: in LF stove, carry out Ca process, in control molten steel, Ca is within target; Control RH vacuum processing time is not less than 20 minutes;
2) to strand heating, control Heating temperature at 1200 ~ 1300 DEG C, control heating rate at 9 ~ 12 minutes/centimetre;
3) carry out the first rough rolling step, the start rolling temperature controlling this stage is not less than 1100 DEG C;
4) through for the first time after temperature, at start rolling temperature is 1000 DEG C ~ 1050 DEG C, subordinate phase roughing is carried out;
5) through for the second time after temperature, at start rolling temperature is 930 DEG C ~ 960 DEG C, carry out finish rolling, controlling finishing temperature is 760 ~ 820 DEG C;
6) heat-treat according to steel plate thickness:
When steel plate thickness is at 10 ~ 20 millimeters, the mode adopting normalizing to add quick cooling+tempering is carried out, and normalizing temperature is 800 ~ 900 DEG C, and the normalizing time is (minute): t+30, and tempering temperature is 600 ~ 680 DEG C, and tempering time is (minute): t+50; In formula: t is the thickness of steel plate, unit is millimeter; When cooling fast, red temperature controls at 400 ~ 600 DEG C;
When steel plate thickness is being greater than 20 to when being no more than 40 millimeters, adopt the mode of quenching+tempering to carry out, quenching temperature is 800 ~ 900 DEG C, and the cool time is (minute): t+30, and tempering temperature is 600 ~ 680 DEG C, and tempering time is (minute): t+50;
In formula: t is the thickness of steel plate, unit is millimeter;
When steel plate thickness is being greater than 40 to when being no more than 60 millimeters, adopt the mode of two quenching+temperings to carry out, quenching temperature is 800 ~ 900 DEG C for the first time, and the cool time is (minute): t+30; Second time quenching temperature is 800 ~ 850 DEG C, and the cool time is (minute): t+30; Tempering temperature is 600 ~ 680 DEG C, and tempering time is (minute): t+50;
In formula: t is the thickness of steel plate, unit is millimeter;
7) stand-by.
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| CN107619999B (en) * | 2017-10-18 | 2019-12-17 | 舞阳钢铁有限责任公司 | hydrogen sulfide corrosion resistant thin steel plate for long time die welding heat treatment and production method thereof |
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| CN113430462B (en) * | 2021-06-25 | 2022-08-30 | 河北普阳钢铁有限公司 | High-strength corrosion-resistant low-carbon alloy steel and preparation method thereof |
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| JPS52127427A (en) * | 1976-04-19 | 1977-10-26 | Kawasaki Steel Co | Production of low temperature steel having good low temperature toughness at welded point |
| JPS58171526A (en) * | 1982-03-31 | 1983-10-08 | Nippon Steel Corp | Manufacture of steel for extra-low temperature use |
| CN101235466A (en) * | 2008-02-28 | 2008-08-06 | 武汉钢铁(集团)公司 | High ductility negative 110 degree low-temperature steel and manufacturing method thereof |
| JP2011105963A (en) * | 2009-11-12 | 2011-06-02 | Nippon Steel Corp | Method for manufacturing low yield ratio high tensile strength steel plate excellent in low temperature toughness |
| CN102330031A (en) * | 2011-10-27 | 2012-01-25 | 武汉钢铁(集团)公司 | High-tenacity -130 DEG C low-temperature steel and manufacturing method thereof |
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