WO2012067474A2 - 극저온 인성이 우수한 고강도 강재 및 그 제조방법 - Google Patents
극저온 인성이 우수한 고강도 강재 및 그 제조방법 Download PDFInfo
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- WO2012067474A2 WO2012067474A2 PCT/KR2011/008884 KR2011008884W WO2012067474A2 WO 2012067474 A2 WO2012067474 A2 WO 2012067474A2 KR 2011008884 W KR2011008884 W KR 2011008884W WO 2012067474 A2 WO2012067474 A2 WO 2012067474A2
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/30—Stress-relieving
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Definitions
- the present invention relates to a manganese and nickel-containing steel used as a structural material for cryogenic storage containers, such as LNG (Liquefied Natural Gas), and a method of manufacturing the same. More specifically, an optimum ratio of low-cost Mn instead of expensive Ni
- the present invention relates to a steel material having excellent cryogenic toughness and high strength at the same time as it is added to the structure, and the microstructure of the structure is refined through control rolling and angle angle and the residual austenite is precipitated by tempering.
- Grain refinement is known to be the only method of processing various metals known to increase the strength and toughness at the same time. This is because when the grains become finer, the density of dislocations accumulated in the grain boundaries is lowered, so that the concentration of stress to neighboring crystals becomes smaller and the fracture strength is not reached, thereby improving the toughness.
- grain refinement that can be obtained by hot control rolling and cooling of TMCP, etc. is about 5 ⁇ m, and at a maximum of about ⁇ 60 ° C. or less, toughness rapidly decreases.
- the toughness rapidly decreases at about -100 ° C.
- cryogenic temperatures of about -165 0 C, such as an LNG storage tag have secured cryogenic toughness by adding Ni and the like at the same time as grain refinement.
- substitutional alloying elements to steel mostly increases strength and lowers toughness.
- Pt, Ni, Ru, Rh, Ir and Re Since toughness is known to be improved, it is conceivable to add such alloying elements, but Ni is the only commercially available element.
- the steels used as cryogenic steels for the last few decades are those containing 9% Ni (hereinafter 9% Ni steel).
- 93 ⁇ 4Ni steels generally produce fine martensite after reheating + something (Q) and then soften martensite by tempering (T) and at the same time precipitate residual austenite to about 15%.
- the fine lath of martensite is recovered by tempering to have a fine structure of several hundred nm, and tens of nm of austenite is generated between the laths, resulting in a total structure of several hundred nm.
- the toughness is improved by the addition of 9% Ni even at cryogenic temperatures.
- 9% Ni steels have been limited in their use due to the addition of expensive Ni, despite their high strength and excellent cryogenic toughness.
- US4257808 is a technology that improves cryogenic toughness by adding 5 n instead of 9% Ni and miniaturizing and tempering grains through four iterative heat treatments in the austenite + ferrite ideal zone temperature range, as disclosed in 997-0043139. Similarly, by adding 13% Mn, the crystal grains are refined and tempered through four iterative heat treatments in the austenite + ferrite ideal temperature zone, thereby improving the cryogenic toughness.
- Another technique is to reduce the Ni in the existing 9% Ni while maintaining the existing 93 ⁇ 4Ni manufacturing process and add Mn and Cr instead.
- JP 2007/080646 is a patent in which Ni content of 5.5% or more is added and Mn and Cr are added 2.0% and 1.5% or less, respectively.
- the patents have to be subjected to repeated heat treatment and tempering four or more times to obtain cryogenic toughness, thereby obtaining a fine structure, and thus, can produce a steel having excellent cryogenic toughness. Therefore, the number of times of heat treatment is Increasingly, there is a problem in that heat treatment costs and loads of heat treatment facilities are generated.
- the present invention is to solve the above problems, having cryogenic toughness
- the steel according to the present invention has a weight of 3 ⁇ 4, carbon (C): 0.01 to 0.06%, manganese (): 2.0 to 8.0%, nickel (Ni): 0.01 to 6.0%, molybdenum (Mo) : 0.02 ⁇ 0.6%, Silicon (Si): 0.03 ⁇ 0.5%, Aluminum (A1): 0.003-0.05%, Nitrogen (N): 0.0015-0. 23 ⁇ 4, Phosphorus (P): 0.02% or less , Sulfur (S ): 0.01% or less, characterized in that it contains the remaining Fe and other impurities.
- Ti titanium
- Cr crumb
- Cu copper
- Mn and Ni satisfy 8 ⁇ 1.5xMn + Ni ⁇ 12.
- the steel has a main martensite of less than 10 vol%
- the manufacturing method of the steel according to the present invention By weight%, carbon (C): 0.01-0.06%, manganese ( ⁇ ): 2.0-8.0%, nickel (Ni): 0.01-6.0%, molybdenum (Mo): 0.02-0.6%, silicon (Si): 0.03 ⁇ 0.53 ⁇ 4, aluminum (A1): 0.003-0.05%, nitrogen (N): 0.0015 ⁇ 0.0W, phosphorus (P): 0.02% or less, sulfur (S): 0.01% or less, containing remaining Fe and other impurities Heating step of heating the steel slab in the temperature range of 1000 ⁇ 1250 ° C ⁇ Rolling step of finishing the heated slab at a reduction ratio of 403 ⁇ 4 or more at a temperature of 950 o C or less, and rolling the rolled steel to 2 0 C / s Cooling step to the temperature below 400 o C at the above angular velocity, the steel material in
- the yield strength is reduced to 500MPa while reducing the expensive Ni content, the cryogenic toughness of the impact energy value of 70J or more at the cryogenic temperature of -196 ° C or less
- This excellent high strength structural steel can be manufactured.
- FIG. 1 is a transmission electron micrograph of the inventive steel according to the present invention, showing a tissue photograph of the invention steel.
- C is the most important element that precipitates as austenite at grain boundaries of old austenite, between laths of martensite, carbides in bainite, etc., and therefore, an appropriate content should be contained in steel.
- the content of c is less than 0.01%, coarse bainite is produced due to lack of hardening ability at the time of quenching after controlled rolling, or the fraction of residual austenite produced when tempering is too small to be less than 3%, thereby decreasing the cryogenic toughness. There is a problem.
- the C content is preferably limited to 0.01 to 0.063 ⁇ 4.
- Si is mainly used as a deoxidizer and is a useful element because of its strength improving effect.
- Si increases the stability of residual austenite and can form a large amount of residual austenite even with a small C content.
- Ni is almost the only element that can simultaneously improve the strength and toughness of the base material. In order to exhibit such an effect, 0.01% or more should be added. However, when 6.0% or more is added, economical efficiency is lowered, so the content of Ni is limited to 6.0% or less. Therefore, the content of Ni is preferably limited to 0.01 to 6.0%.
- Mo can greatly improve the hardenability even with a small amount of addition, thereby miniaturizing the structure of martensite, and greatly improving the stability of residual austenite, thereby improving cryogenic toughness.
- segregation at the grain boundaries of P and the like is suppressed to suppress grain boundary fracture.
- the Mo content is 0.02-0.6% It is desirable to limit. It is more preferable that the content of Mo for toughness is 5 to 103 ⁇ 4> of the added Mn content while satisfying the range of 0.02-0.6%.
- P is an element that is advantageous in improving strength and corrosion resistance, but greatly inhibits layer toughness. It is advantageous to keep the content as low as possible as it is an element.
- A1 is an element that can deoxidize molten steel at low cost, it is preferable to add 0.003% or more.However, when A1 is added in excess of 0.05%, it causes nozzle clogging during continuous casting and encourages formation of island martensite during welding. , It is harmful to the fracture toughness of the weld, it is preferable to limit the content of A1 to 0.003 ⁇ 0.055). Nitrogen (N) :(). 0015-0.
- N increases the fraction and stability of the retained austenite to improve the cryogenic toughness, but it is necessary to limit the content to 0.0 or less since it is solid-solubilized again in the weld heat affected zone and greatly reduces the cryogenic toughness.
- controlling the N content to less than 0.0015% increases the load on the steelmaking process, the content of N is limited to 0.0015% or more in the present invention.
- the above-described steel having the advantageous emphasis of the present invention can obtain a sufficient effect even by including the alloying elements in the above-described content range, but the characteristics such as the strength and toughness of the steel, the toughness and weldability of the weld heat affected zone, etc.
- Ti titanium
- Cr chromium
- Cu copper
- Ti suppresses the growth of crystal grains upon heating and greatly improves low temperature toughness.
- 0.003% or more must be added, When added in excess of 0.05%, there is a problem of a decrease in low temperature toughness due to clogging of the playing nozzle or crystallization of the center part, and the content of Ti is preferably limited to 0.003-0.05%. Creme (0): 0.1-5.0>
- Cr has the effect of increasing the hardenability like Ni and Mn, and it is necessary to add more than 0.1% to make the martensite after control angle. However, when adding 5.03 ⁇ 4 or more, the weldability is greatly reduced, and the content of Cr is preferably limited to 0.1 to 5.0%. Copper (Cu): 0.1 ⁇ 3.0%
- Cu is an element that can increase the strength while minimizing the toughness of the base metal. In order to exhibit such effects, it is preferable to add 0.1% or more, but when excessively added in excess of 3.0%, the surface quality of the product is greatly inhibited, and the content of Cu is preferably limited to 0.1 to 3.0%. .
- the microstructure of the steel of the present invention preferably has a martensite composed of martensite or a residual austenite of 3-15% in a phase in which martensite and 10% or less bainite are common.
- microstructures are those in which the columnar phase consists of dry tencite of lath structure or has a residual austenite of 3 to 15> in which martensite and less than 10% of bainite are common.
- Figure 1 shows the microstructure of the steel of the present invention, the part shown in white in the picture is a retained austenite, the part shown in black is a tempered martensite lath.
- the microstructure of the steel of the present invention has a few hundred nanoscale residual austenite between the fine martensite lath transformed from austenite of 50um or less or in martensite and bainite It is desirable to have a tissue that distributes.
- the fine martensitic race structure and the residual austenite that is finely segmented makes the toughness excellent at cryogenic temperatures.
- the manufacturing method of the steel material of this invention as mentioned above is demonstrated.
- the steel slab having the above composition is heated, followed by rolling to stretch the austenite evenly, and then cooling it to form fine martensite or fine martensite and fine bainite at a volume fraction of 10% or less. And then tempering to finely disperse and precipitate the residual austenite of 33 ⁇ 4 or more between martensite lath or between martensite lath and in bainite to produce steel having excellent cryogenic toughness.
- the slab heating is preferably made at a temperature of 1050 ⁇ 1250 ° C.
- the slab heating temperature requires heating above 1050 ° C in order to solidify Ti carbonitrides formed during casting and homogenize the carbon spout, but coarse austenite when heated to excessively high temperatures above 1250 ° C. Since there is a fear that, the heating temperature is preferably made at 1050 ⁇ 1250 ° C.
- the heated slab is preferably subjected to rough rolling at 1000-1250 ° C. after heating to adjust its shape.
- the casting structure such as dendrites formed during casting by rolling is destroyed, and the effect of reducing the size of austenite can also be obtained.
- the rough rolling temperature becomes too low below 1000 o C, the strength of the steel is greatly increased.
- the rough rolling temperature is higher than 1250 ° C., the austenitic grains in the material become coarse during the rolling process, and thus the low-temperature toughness is lowered. It is preferably made at a temperature of 1000 ⁇ 1250 ° C.
- finishing rolling is performed at a temperature of 950 ° C. or lower.
- the austenite grains are elongated in the form of pancakes, so that the austenite grains can be miniaturized.
- the temperature of the finishing rolling is made at 700 to 950 ° C.
- the amount of rolling reduction during finishing rolling is 40% or more of the austenite to be stretched evenly. After the finishing rolling, it is cooled at an angle of incidence of 2 ° C / s or more.
- the stretched austenite can be transformed into coarse bainite, which can be transformed into mostly martensite or martensite and some fine bainite.
- each end temperature it is preferable to limit each end temperature to 400 ° C or less.
- After the cooling is preferably tempered for 0.5 to 4 hours at a temperature of 550 ⁇ 650 ° C.
- fine austenite is formed from cementite in the fine martensite class or bainite. It is created and remains unchanged for the next time. That is, austenite is present between the fine martensite laths or between the martensite laths and in the bainite.
- the tempering temperature will be above 650 o C
- Tempering at temperatures of 550-650 ° C. for 0.5-4 hours is preferred.
- Table 3 shows the physical property test results of the rolled, squared, and heat-treated slabs prepared under the conditions of Table 1 below.
- Table 3 the yield strength, tensile strength, and elongation are measured by uniaxial tensile test, and the cryogenic lamella energy value is -196 0 C at Charpy V-notch lamella test.
- each element in Table 1 represents the weight%, as described above, in Table 1, the steel that satisfies the composition of the steel that is the subject of the present invention, that is, the steel outside the composition range of the invention steel 1-6 and the present invention, That is, comparative steels 1-6 were described.
- Inventive materials 1 to 6 of the conditions described in Table 2 were prepared under conditions consistent with the rolling and heat treatment methods of the present invention as described above.
- the comparative materials 1-15 show what was manufactured on the conditions which do not correspond with the conditions of this invention.
- Comparative materials 7 to 15 show that the steel materials (inventive steels 1, 2, 3 and 6) satisfying the above-described composition range of the present invention were manufactured under conditions that do not conform to the rolling and heat treatment methods of the present invention.
- Comparative materials 1 to 6 are manufactured to steel (comparative steel 1 to 6) that does not satisfy the composition range of the present invention under the conditions of the rolling and heat treatment method of the present invention.
- Bainite austenitic yield steel tensile steel elongation *
- Comparative Material 1 Comparative Steel 1 82.6 4.6 477 587 28.1 21 C Less than Comparative C 2 Comparative Steel 2 2,5 12.8 678 916 16.3 More than 5 C Comparative Material 3 Comparative Steel 3 37.5 4.4 548 606 25.3 42 Mn Ni Below Comparative Material 4 Comparative Steel 4 0.5 4.2 654 764 20.9 19 Less than Mo Comparative 5 Comparative Steel 5 2.1 6.1 667 786 17.4 53 Mn Ni Excess Comparative 6 Comparative Steel 6 2.6 4.3 652 770 20.9 22 Mn Ni Excess Comparative 7 Inventive Steel 2 0.4 8.4 623 732 21.6 21 Rolling start exceeded Comparative material 8 Inventive steel 3 1.5 7.4 673 889 17.4 23 Rolling finish temperature not compared Comparative material 9 Invented steel 6 0.2 3.2 639 748 22.7 54 Less than rolling reduction Comparative material 10 Inventive steel 2 79.0 6.7 666 776 24.2 22 ⁇ Less than angular velocity comparative material 11 Invention Steel 3 9
- Comparative Materials 1 and 2 are prepared with the compositions of Comparative Steels 1 and 2, respectively, and represent a case where the content of C is less than or exceeded. In the case of Comparative Material 1, the content of C is less than the content of the present invention. At the time of rolling after rolling, the fine lathic martensite was not produced and transformed into bainite without coarse carbide, yield strength and tensile strength. Is low and is insufficient to be used as a structural material.
- Comparative Material 2 In addition, in the case of Comparative Material 2, the content of C exceeds the content of the present invention, while the strength increases greatly as the carbon content increases, while the lamellar energy value does not reach the range of the invention, thus inferior to cryogenic toughness. You can check it. Comparative materials 3, 5 and 6 are prepared in the composition of comparative steels 3, 5 and 6, respectively, showing a case where the 1.5xMn + Ni content is outside the scope of the invention.
- Comparative Material 3 the value of 1.5xMn + Ni is less than 8, and since the hardenability of the steel grade is poor, martensite is not refined at the time of transformation and transforms into coarse bainite, so that the cryogenic toughness Inferior.
- Comparative material 4 is a steel material having a composition of Comparative steel 4 and added with a Mo content smaller than the range of the invention, and thus it is insufficient to suppress brittleness due to segregation of P which is an unavoidable impurity in manufacturing.
- the comparative materials 7 and 8 each have the composition of the invention steels 2 and 3, so that the composition is within the scope of the invention, but the start and end temperatures of the finishing rolling temperature are outside the scope of the invention.
- the comparative material 7 had a case where the filament rolling temperature was higher than the range of the invention, and the grains of austenite were coarsened, and thus the cryogenic toughness did not meet the criterion.
- the comparative material 8 having a low finishing rolling temperature the rolling load increased sharply, making it difficult to manufacture, and the manufactured steel also had a great increase in strength, resulting in inferior cryogenic toughness.
- the comparative material 9 has the composition of the invention steel 6 and the composition is within the scope of the invention, but the total residual reduction in finishing rolling is smaller than the scope of the invention.
- the comparative material 10 has the composition of the invention steel 2, but the composition is within the range of the invention, but the angular velocity after finishing rolling is lower than the range of the invention.
- the deformed austenite after rolling has to be transformed into fine martensite or fine bainite by an acceleration angle to have a fine structure, so that the cryogenic toughness is excellent.
- the comparative material 11 has the composition of invention steel 3, and although a composition exists in the range of invention, when each end temperature is outside the range of invention. In the case of 11 of the comparative material whose end temperature is lower than the range of the invention, austenite is not sufficiently transformed to martensite during acceleration angle, but transformed into ferrite or coarse bainite, resulting in the final structure. Becomes coarse. Thus, only the coarse bainite with coarse cementite is transformed into coarse microstructure, resulting in inferior cryogenic toughness.
- Comparative materials 12 and 13 have the compositions of inventive steels 6 and 2, respectively, and the composition is within the scope of the invention, but the tempering heat treatment temperature is outside the scope of the invention.
- Comparative Material 12 having a tempering temperature lower than the range of the invention the formation of residual austenite in the martensite and bainite transformed during the acceleration angle was slowed, and the softening of martensite and bainite itself was insufficient. Therefore, the strength is greatly increased, but the ductility is reduced, the cryogenic toughness is inferior.
- Comparative Material 13 when the tempering temperature is high, the formation of residual austenite becomes excessive and some austenite is reversely transformed back to martensite at the time of re-heating to room temperature or cryogenic temperature, and also easily at tension or delamination. It will transform organic into martensite. As a result, tensile strength and elongation increase greatly, but the cryogenic toughness is inferior. Comparative materials 14 and 15 have the compositions of Inventive Steels 1 and 2, respectively, and the composition is within the scope of the invention, but the tempering time is outside the scope of the invention.
- the tempering time was shorter than the range of the invention, so that the formation of residual austenite in the martensite and bainite transformed during the accelerated cooling was insufficient, and the softening of the martensite and bainite itself was insufficient.
- the strength is significantly higher, but the ductility is reduced, resulting in inferior cryogenic toughness.
- the tempering time is long as in Comparative Material 15, as in Comparative Material 13, residual austenite is excessively produced, and some austenite is inversely transformed into martensite again at room temperature or cryogenic temperature. Or it is easily transformed organically to martensite during impact deformation. As a result, tensile strength and elongation increase greatly, but the cryogenic toughness is inferior.
- the steel produced by the present invention is produced by the production method of the present invention, it is generally used even if the expensive Ni content is reduced. It was confirmed that there is an excellent effect on the cryogenic steel equivalent to 9% Ni. As described above, when the steel prepared by the present invention was manufactured by the manufacturing method of the present invention, it was confirmed that there is an excellent effect on the cryogenic steel equivalent to 93 ⁇ 4Ni, which is generally used even though the expensive Ni content is reduced.
- the present invention by optimally controlling the alloy composition and rolling, engraving, and heat treatment method, it is possible to effectively manufacture high-strength structural steel with excellent cryogenic toughness, which is an important characteristic of cryogenic steel, while reducing expensive Ni content. .
Abstract
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Priority Applications (5)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP11841040.6A EP2641987B1 (en) | 2010-11-19 | 2011-11-21 | High-strength steel material having outstanding ultra-low-temperature toughness and a production method therefor |
JP2013539774A JP5820889B2 (ja) | 2010-11-19 | 2011-11-21 | 極低温靭性に優れた高強度鋼材及びその製造方法 |
ES11841040.6T ES2581335T3 (es) | 2010-11-19 | 2011-11-21 | Material de acero de alta resistencia que tiene una dureza sobresaliente a temperatura ultrabaja y método de producción del mismo |
CN201180055708.1A CN103221562B (zh) | 2010-11-19 | 2011-11-21 | 具有优异的超低温韧性的高强度钢材料及其制备方法 |
US13/824,647 US9394579B2 (en) | 2010-11-19 | 2011-11-21 | High-strength steel material having outstanding ultra-low-temperature toughness and a production method therefor |
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JP (1) | JP5820889B2 (ko) |
KR (1) | KR101271974B1 (ko) |
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Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
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WO2014092129A1 (ja) * | 2012-12-13 | 2014-06-19 | 株式会社神戸製鋼所 | 極低温靭性に優れた厚鋼板 |
JP2014118579A (ja) * | 2012-12-13 | 2014-06-30 | Kobe Steel Ltd | 極低温靭性に優れた厚鋼板 |
CN104854252A (zh) * | 2012-12-13 | 2015-08-19 | 株式会社神户制钢所 | 极低温韧性优异的厚钢板 |
JP2014125678A (ja) * | 2012-12-27 | 2014-07-07 | Kobe Steel Ltd | 極低温靱性に優れた厚鋼板 |
CN114645216A (zh) * | 2022-03-25 | 2022-06-21 | 宝武杰富意特殊钢有限公司 | 模具钢及其制备方法 |
CN116987974A (zh) * | 2023-08-14 | 2023-11-03 | 东北大学 | 一种高强度高韧性的低磁导率中锰钢及其制造方法 |
CN116987974B (zh) * | 2023-08-14 | 2024-04-09 | 东北大学 | 一种高强度高韧性的低磁导率中锰钢及其制造方法 |
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WO2012067474A3 (ko) | 2012-09-13 |
JP5820889B2 (ja) | 2015-11-24 |
JP2014501848A (ja) | 2014-01-23 |
CN103221562B (zh) | 2016-07-06 |
US9394579B2 (en) | 2016-07-19 |
US20130174941A1 (en) | 2013-07-11 |
EP2641987A4 (en) | 2014-11-12 |
KR20120054359A (ko) | 2012-05-30 |
ES2581335T3 (es) | 2016-09-05 |
EP2641987A2 (en) | 2013-09-25 |
KR101271974B1 (ko) | 2013-06-07 |
CN103221562A (zh) | 2013-07-24 |
EP2641987B1 (en) | 2016-04-06 |
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