CN105624553B - High-strength steel plate with improved low-temperature impact toughness and manufacturing method thereof - Google Patents

High-strength steel plate with improved low-temperature impact toughness and manufacturing method thereof Download PDF

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CN105624553B
CN105624553B CN201511019835.2A CN201511019835A CN105624553B CN 105624553 B CN105624553 B CN 105624553B CN 201511019835 A CN201511019835 A CN 201511019835A CN 105624553 B CN105624553 B CN 105624553B
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steel
rare earth
temperature
steel plate
slag
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CN105624553A (en
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赖朝彬
陈英俊
冯小明
孙乐飞
操瑞宏
汪志刚
邓志豪
习小军
吴绍杰
付军
赵和明
袁传泉
傅清霞
王国文
杨清
朱福生
吴春红
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Jiangxi University of Science and Technology
Xinyu Iron and Steel Co Ltd
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Jiangxi University of Science and Technology
Xinyu Iron and Steel Co Ltd
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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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/0006—Adding metallic additives
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/04—Removing impurities by adding a treating agent
    • C21C7/06—Deoxidising, e.g. killing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/04—Removing impurities by adding a treating agent
    • C21C7/064—Dephosphorising; Desulfurising
    • 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
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • C22C33/06—Making ferrous alloys by melting using master alloys
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • 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
    • 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
    • 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
    • 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
    • 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
    • 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
    • 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
    • C21D2211/005—Ferrite
    • 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
    • C21D2211/009—Pearlite

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

The invention discloses a high-strength steel plate with improved low-temperature impact toughness. The high-strength steel plate is manufactured from the chemical ingredients comprising, by mass percent, 0.07% to 0.19% of C, 0.15% to 0.45% of Si, 1.15% to 1.65% of Mn, not larger than 0.025% of P, not larger than 0.008% of S, not larger than 0.04% of Nb, not larger than 0.20% of V, not larger than 0.015% of Ti, 0.005% to 0.030% of Alt, not larger than 0.020% of N, 0.002% to 0.003% of O, 0.005% to 0.010% of Y, 0.015% to 0.025% of Ce and the balance Fe, rare earth and inevitable impurities. The rare earth is yttrium-based rare earth, and a composite inclusion component in steel comprises, by mass percent, 25.72% to 69.15% of Y and 3.09% to 17.52% of Ce. The matrix structure of the steel plate is a fine ferritic and pearlitic structure. The yttrium-based rare earth is used for achieving the functions of purifying, denaturating, microalloying and oxide metallurgy in the steel, and the low-temperature impact toughness of the high-strength steel plate is improved.

Description

A kind of high-strength steel sheet and its manufacture method for improving low-temperature impact toughness
Technical field
The present invention relates to a kind of high-strength steel sheet and its manufacturing technology, more particularly to a kind of height for improving low-temperature impact toughness Strength steel sheet and its manufacture method.
Background technology
With the development and technological progress of society, every profession and trade it is also proposed requirements at the higher level to the performance of steel plate used by itself, For the deadweight of lightening material, it is desirable to which steel plate has higher intensity；In order to expand the use environment and application of material, Steel plate is asked to have good low-temperature flexibility；The manufacture processing of material, also requires that steel plate has certain solderability for convenience, because This, the demand of high strength steel plate is increasing.High-strength steel sheet typically refers to steel plate of the yield strength more than 315MPa, is making Ship, ocean platform, building structure, bridge, pressure vessel, the application of oil-gas pipeline field are very universal.Particularly ship and ocean Platform, marine environment are severe, in addition to gravitational load is born, it is contemplated that wind load, seaway load, ocean current load, ice load Deng impact, user expect while proof strength, impact flexibility be particularly low-temperature impact toughness the higher the better.Existing refining Steel technological progress, although oxygen, sulfur in steel can be controlled in relatively low scope, but still unavoidably there are some defects：It is all As component segregation of continuous casting slab, sulfide, oxide are separated out in crystal boundary, calcium aluminate, Manganese monosulfide., magnesium oxide, alumina inclusion are formed Thing, if inner inclusion owner strip MnS, a small amount of string-like Al after this continuous casting billet milling2O3And aluminate, these field trashes The impact that side knock performance is particularly to impact property is very big, and further removal of inclusions improves low-temperature impact toughness Means are limited.For this purpose, a kind of excellent high-strength steel sheet of low temperature (less than -40 DEG C) impact flexibility of research and its manufacture method, are The direction that metallargist makes great efforts.
The content of the invention
For the problem that prior art is present, it is an object of the invention to provide it is a kind of using Yttrium base rare earth silicon calcium alloy come Cleaning molten steel, strengthens inclusion modification, refines matrix, and so as to the one kind for improving low-temperature impact toughness, to improve low-temperature impact tough The high-strength steel sheet and its manufacture method of property.
A kind of high-strength steel sheet for improving low-temperature impact toughness, its chemical composition is by weight percent：C：0.07%～ 0.19%, Si：0.15%～0.45%, Mn：1.15%～1.65%, P≤0.025%, S≤0.008%, Nb≤0.04%, V ≤ 0.20%, Ti≤0.015%, Ni≤0.40%, Cr≤0.10%, Cu≤0.10%, Mo≤0.08%, Alt：0.005% ～0.030%, N≤0.020%, O：0.002%～0.003%, its balance of ferrum Fe, rare earth and inevitable impurity, its Be characterised by, the rare earth be Yttrium base rare earth, solid solution Y in steel：0.005%～0.010%, solid solution Ce：0.015%～ 0.025%；Remain field trash to exist with the complex inclusion form that Y, Ce and O, Mg, Al, S combine to form small and dispersed in steel, In the complex inclusion component comprising Y, Ce mass percent it is：Y：25.72%～69.15%, Ce：3.09%～ 17.52%；Steel matrix is organized as tiny ferrite+pearlitic structrure.
CaS field trash is included in the complex inclusion component also.
The general thought of the present invention is by adding Yttrium base rare earth silicon calcium alloy promoting in steel on the basis of conventional steel grade Field trash faster floats, and further effective control residual sulfide, oxide form, eliminates MnS field trashes harm in steel Effect, makes Yttrium base rare earth that the effect of purification, degeneration, microalloying and Oxide Metallurgy is played in steel, finally stays in steel The complex inclusion based on Y, supplemented by Ce of Y, Ce simple substance and small and dispersed, this matrix greatly improve steel plate low temperature Impact flexibility.
A kind of manufacture method of the high-strength steel sheet for being exclusively used in improving low-temperature impact toughness, its processing step：
1), converter smelting：Smelted using top and bottom complex blowing oxygen coverter, the deoxidation alloying in tapping process, oxygen contain Amount control is in 32～68ppm；
2), LF stoves refine：After molten steel enters refine station, argon bottom-blowing, while Calx, refining slag and submerged arc slag are added, Be then electrified to heat up, heat up 8 minutes after, thermometric, sampling carry out trimming, at the same according to top slag situation, add carbide with Aluminum shot makes white slag, and the white slag retention time is more than 15 minutes, then carries out thermometric, sampling again, finely tunes alloying component, treat molten steel temperature After degree, composition are up to standard, calcium line is fed, after 1～2 minute, then with the speed feeding Yttrium base rare earth silicon calcium alloy claded wire of 2～3m/s 300m～500m, line feeding carry out soft blow argon after terminating, soft argon blowing time 8～15 minutes promotes field trash fully to float and enters molten Slag, obtains molten steel composition its mass percent in following scope：C：0.07%～0.19%, Si：0.15%～0.45%, Mn： 1.15%～1.65%, P≤0.025%, S≤0.008%, Nb≤0.04%, V≤0.20%, Ti≤0.015%, Ni≤ 0.40%, Cr≤0.10%, Cu≤0.10%, Mo≤0.08%, Alt：0.005%～0.030%, N≤0.020%, O： 0.002%～0.003%, solid solution Y in steel：0.005%～0.010%, solid solution Ce：0.015%～0.025%；Remain in steel Field trash is present with the complex inclusion form that Y, Ce and O, Mg, Al, S combine to form small and dispersed, the complex inclusion group In point comprising Y, Ce mass percent it is：Y：25.72%～69.15%, Ce：3.09%～17.52%；Its balance of ferrum Fe and Inevitable impurity；
3), continuous casting：Refine terminates, and molten steel is sent to continuous casting workshop carries out being casting continuously to form slab, and 1515 DEG C of tundish temperature～ 1540 DEG C, in 0.72～0.90m/min, secondary cooling water adopts weak cold, air-water spraying cooling to slab casting speed control；
4), heating cycle：Continuous casting billet is heated to into 1215～1236 DEG C in heating furnace, heating total time by 1.15～ 1.25 minutes/mm is controlled, temperature retention time >=185min；
5), rolling mill practice：Rolled using two-stage control, start rolling temperature >=1060 DEG C of recrystallization zone rolling, recrystallization Area rolls every time reduction ratio and controls 28%～38%, and middle base treats temperature, the open rolling temperature of Unhydrated cement rolling on roller-way 840～880 DEG C of degree, 808～838 DEG C of finishing temperature, the accumulative reduction ratio of Unhydrated cement are controlled 58%～68%；
6), roller repairing technique：Stack slow cooling using concentrating after hot-rolled steel plate, its matrix be tiny ferrite+ Pearlitic structrure, in steel plate, field trash is present with the complex inclusion form that Y, Ce and O, Mg, Al, S combine to form small and dispersed.
It is an advantage of the current invention that by Yttrium base rare earth silicon calcium alloy is added in steel, using Y, Ce in rare earth preferentially with steel in Oxygen, the impurity element such as the sulfur complex rare-earth oxidate containing valuable metal, rare earth complex sulfide and the rare earth composite oxygen that generate after reacting Sulfide, the little advantage of rare earth complex inclusion density ratio lanthanum of the formation based on yttrium, cerium mischmetal complex inclusion density, plus Fast steel inclusion floats, and reduces impurity in steel.And further with Y, Ce effective control residual sulfide, oxide shape State, eliminates MnS field trash damaging effects in steel, makes Yttrium base rare earth that purification, degeneration, microalloying and oxide smelting are played in steel The effect of gold, finally leaves the complex inclusion based on Y, supplemented by Ce of Y, Ce simple substance and small and dispersed in steel, this Complex inclusion form and tiny ferrite+pearlitic structrure, greatly improve steel plate low-temperature impact toughness.
Description of the drawings
Fig. 1 is the EH36 deck of boat metallographic structures of steel containing yttrium element of the invention.
Fig. 2 amplifies 100 times of lower patterns for field trash at the slab thickness of steel containing yttrium element 1/4 of the invention.
Fig. 3 is field trash 5000 times of lower patterns of amplification in Fig. 2.
Fig. 4 is side knock fracture field trash pattern at the EH36 decks of boat of steel containing yttrium element thickness 1/2 of the invention.
Fig. 5 is impact of collision fracture field trash pattern at the EH36 decks of boat of steel containing yttrium element thickness 1/2 of the invention.
Fig. 6 is -80 DEG C of impact fracture patterns in longitudinal direction at the EH36 decks of boat of steel containing yttrium element thickness of the invention 1/4.
Fig. 7 is Transverse at the EH36 decks of boat of steel containing yttrium element thickness 1/4 of the invention to -80 DEG C of impact fracture patterns.
Fig. 8 is without -80 DEG C of impact fracture patterns (comparative example) in longitudinal direction at rare earth steel EH36 decks of boat thickness 1/4.
Fig. 9 is to -80 DEG C of impact fracture forms (comparative example) without Transverse at rare earth steel EH36 decks of boat thickness 1/4.
Specific embodiment：
The invention will be further described with reference to the accompanying drawings and examples, and in embodiment, high-strength steel sheet is the present invention Prepared by designed chemical composition, manufacture method.
Technical scheme 1：A kind of high-strength steel sheet for improving low-temperature impact toughness of the present invention, is rolled using TMCP, Production CCSEH36 high strength steel plate for ship building, its chemical composition are controlled by following mass percent：C：0.07%～0.13%, Si： 0.15%～0.30%, Mn：1.15%～1.45%, P≤0.025%, S≤0.006%, Nb≤0.04%, V≤0.005%, Ti：0.008%～0.015%, Ni≤0.10%, Cr≤0.10%, Cu≤0.10%, Mo≤0.08%, Alt：0.015%～ 0.030%, N≤0.015%, O：0.002%～0.003%, solid solution Y in steel：0.005%～0.008%, solid solution Ce： 0.015%～0.023%；The complex inclusion that field trash combines to form small and dispersed with Y, Ce and O, Mg, Al, S is remained in steel Form is present, and in the complex inclusion component comprising Y, Ce mass percent is：Y：25.72%～67.92%, Ce： 3.09%～15.27%；CaS field trash is included in the complex inclusion component also；Its balance of ferrum Fe and inevitably Impurity；Steel matrix is organized as tiny ferrite+pearlitic structrure.
The manufacture method of the CCSEH36 decks of boat described in technical scheme 1, its processing step：
1), converter smelting：Smelted using top and bottom complex blowing oxygen coverter, the deoxidation alloying in tapping process, oxygen contain Amount control is in 35～65ppm；
2), LF stoves refine：After molten steel enters refine station, argon bottom-blowing, while Calx, refining slag and submerged arc slag are added, Be then electrified to heat up, heat up 9 minutes after, thermometric, sampling carry out trimming, at the same according to top slag situation, add carbide with Aluminum shot makes white slag, and the white slag retention time is more than 15 minutes, then carries out thermometric, sampling again, finely tunes alloying component, treat molten steel temperature After degree, composition are up to standard, calcium line is fed, after 2 minutes, then with the speed feeding Yttrium base rare earth silicon calcium alloy claded wire of 2～3m/s 300m～500m, line feeding carry out soft blow argon after terminating, soft argon blowing time 8～15 minutes promotes field trash fully to float and enters molten Slag, obtains molten steel composition its mass percent in following scope：C：0.07%～0.13%, Si：0.15%～0.30%, Mn： 1.15%～1.45%, P≤0.025%, S≤0.006%, Nb≤0.04%, V≤0.005%, Ti：0.008%～ 0.015%, Ni≤0.10%, Cr≤0.10%, Cu≤0.10%, Mo≤0.08%, Alt：0.015%～0.030%, N≤ 0.015%, O：0.002%～0.003%, solid solution Y in steel：0.005%～0.008%, solid solution Ce：0.015%～ 0.023%；Remain field trash to exist with the complex inclusion form that Y, Ce and O, Mg, Al, S combine to form small and dispersed in steel, In the complex inclusion component comprising Y, Ce mass percent it is：Y：25.72%～67.92%, Ce：3.09%～ 15.27%；CaS field trash is included in the complex inclusion component also；Its balance of ferrum Fe and inevitable impurity；
3), continuous casting：Refine terminates, and molten steel is sent to continuous casting workshop carries out being casting continuously to form slab, and 1518 DEG C of tundish temperature～ 1538 DEG C, in 0.73～0.86m/min, secondary cooling water adopts weak cold, air-water spraying cooling to slab casting speed control；
4), heating cycle：Continuous casting billet is heated to into 1218～1234 DEG C in heating furnace, heating total time by 1.18～ 1.23 minutes/mm is controlled, temperature retention time >=190min；
5), rolling mill practice：Rolled using two-stage control, start rolling temperature >=1062 DEG C of recrystallization zone rolling, recrystallization Area rolls every time reduction ratio and controls 28%～38%, and middle base treats temperature, the open rolling temperature of Unhydrated cement rolling on roller-way 845～875 DEG C of degree, 815～835 DEG C of finishing temperature, the accumulative reduction ratio of Unhydrated cement are controlled 58%～68%；
6), roller repairing technique：Cooled down with the rate of cooling of 6.0～12 DEG C/S after hot-rolled steel plate, slowed down using heap is concentrated Cold, its matrix is tiny ferrite+pearlitic structrure, and in steel plate, field trash is combined to form with Y, Ce and O, Mg, Al, S The complex inclusion form of small and dispersed is present.
Technical scheme 2：A kind of high-strength steel sheet for improving low-temperature impact toughness of the present invention, using controlled rolling+normalizing Heat treatment, produces P460NL2 high-strength pressure vessel plates, and its chemical composition is controlled by following mass percent：C：0.15%～ 0.19%, Si：0.25%～0.45%, Mn：1.30%～1.65%, P≤0.015%, S≤0.005%, Nb≤0.02%, V：0.14%～0.18%, Ti≤0.008%, Ni：0.16%～0.39%, Cr≤0.10%, Cu≤0.10%, Mo≤ 0.08%, N：0.006%～0.018%, Alt：0.005%～0.015%, O：0.002%～0.003%, solid solution Y in steel： 0.007%～0.010%, solid solution Ce：0.018%～0.025%；Remain field trash to be combined with O, Mg, Al, S with Y, Ce in steel The complex inclusion form for forming small and dispersed is present, and in the complex inclusion component comprising Y, Ce mass percent is：Y： 30.19%～69.15%, Ce：4.10%～17.52%；Its balance of ferrum Fe and inevitable impurity；Steel matrix is organized For tiny ferrite+pearlitic structrure.
The manufacture method of P460NL2 high-strength pressure vessels plate, its processing step described in technical scheme 2：
1), converter smelting：Smelted using top and bottom complex blowing oxygen coverter, the deoxidation alloying in tapping process, oxygen contain Amount control is in 32～66ppm；
2), LF stoves refine：After molten steel enters refine station, argon bottom-blowing, while Calx, refining slag and submerged arc slag are added, Be then electrified to heat up, heat up 8 minutes after, thermometric, sampling carry out trimming, at the same according to top slag situation, add carbide with Aluminum shot makes white slag, and the white slag retention time is more than 15 minutes, then carries out thermometric, sampling again, finely tunes alloying component, treat molten steel temperature After degree, composition are up to standard, calcium line is fed, after 1 minute, then with the speed feeding Yttrium base rare earth silicon calcium alloy claded wire of 2～3m/s 300m～500m, line feeding carry out soft blow argon after terminating, soft argon blowing time 8～15 minutes promotes field trash fully to float and enters molten Slag, obtains molten steel composition its mass percent in following scope：C：0.15%～0.19%, Si：0.25%～0.45%, Mn： 1.30%～1.65%, P≤0.015%, S≤0.005%, Nb≤0.02%, V：0.14%～0.18%, Ti≤0.008%, Ni：0.16%～0.39%, Cr≤0.10%, Cu≤0.10%, Mo≤0.08%, N：0.006%～0.018%, Alt： 0.005%～0.015%, O：0.002%～0.003%, solid solution Y in steel：0.007%～0.010%, solid solution Ce：0.018% ～0.025%；Remain field trash to deposit with the complex inclusion form that Y, Ce and O, Mg, Al, S combine to form small and dispersed in steel In the complex inclusion component comprising Y, Ce mass percent it is being：Y：30.19%～69.15%, Ce：4.10%～ 17.52%；Its balance of ferrum Fe and inevitable impurity；
3), continuous casting：Refine terminates, and molten steel is sent to continuous casting workshop carries out being casting continuously to form slab, and 1516 DEG C of tundish temperature～ 1536 DEG C, in 0.75～0.85m/min, secondary cooling water adopts weak cold, air-water spraying cooling to slab casting speed control；
4), heating cycle：Continuous casting billet is heated to into 1216～1232 DEG C in heating furnace, heating total time by 1.16～ 1.22 minutes/mm is controlled, temperature retention time >=200min；
5), rolling mill practice：；Rolled using two-stage control, start rolling temperature >=1065 DEG C of recrystallization zone rolling, recrystallization Area rolls every time reduction ratio and controls 28%～38%, and middle base treats temperature, the open rolling temperature of Unhydrated cement rolling on roller-way 850～870 DEG C of degree, 810～832 DEG C of finishing temperature, the accumulative reduction ratio of Unhydrated cement are controlled 58%～68%；
6), roller repairing technique：Cooled down with the rate of cooling of 7.0～15 DEG C/S after hot-rolled steel plate, slowed down using heap is concentrated Cold, its matrix is tiny ferrite+pearlitic structrure, and in steel plate, field trash is combined to form with Y, Ce and O, Mg, Al, S The oxide of small and dispersed, sulfide, oxysulfide duplex impurity form are present.
The present invention is shown in Table 1 in the Yttrium base rare earth silicon calcium alloying component of LF stoves refining procedure input.
1 Yttrium base rare earth silicon calcium alloy composition of table, wt%
Composition Re(Y/Re>80%) Si Ca Fe
Content 25.15 39.39 1.42 28.14
Effect of the Yttrium base rare earth silicon calcium alloy in steel, effect are fully disclosed in patent No. ZL200510019201.7, Here repeat no more.
In process of producing product described in technical scheme 1,2, in LF stove refining procedures, Yttrium base rare earth silicon calcium alloy cored is fed Line, first, in Yttrium base rare earth Y, Ce preferentially with steel in oxygen, the impurity element such as sulfur react after the rare earth combined oxidation that generates Thing, rare earth complex sulfide and rare earth are combined oxysulfide, form the rare earth complex inclusion based on heavy rare earth yttrium, root According to information disclosed in patent No. ZL200510019201.7, YOS complex inclusions density about 4.25g/cm3, it is more multiple than Ce (La) OS Co-clip dopant density about 6.0g/cm3It is much smaller, YOS complex inclusions in steel ascent rate than Ce (La) OS complex inclusions In steel, ascent rate is doubled, and accelerates the middle inclusion floating of steel, is effectively reduced impurity in steel, has been purified molten steel.Secondly, The further effective control residual sulfide of Y, Ce, oxide form in rare earth, degeneration is spherical, and size is less, makes steel Central Plains There is inclusion modification for the compound folder of the higher rare-earth sulfide based on yttrium of fusing point, rare-earth oxide sulfate and rare earth oxide Miscellaneous (see Fig. 2, Fig. 3), can be seen that MnS field trashes damaging effect in steel from Fig. 2, Fig. 3 and eliminates.Finally, by oxide smelting The effect of gold, Y, Ce and oxygen combination can form the fine oxide of a large amount of Dispersed precipitates and are mingled with and be distributed in steel, in austenite Crystal boundary forms pinning effect, so as to refine texture, forms tiny ferrite+pearlitic structrure (see Fig. 1), this matrix Tissue greatly improves steel plate low-temperature impact toughness.
According to 1 produced CCSEH36 high strength steel plate for ship building example strand of technical scheme into table 2 is respectively in, slab thickness is corresponded to At 1/4, Yttrium base rare earth complex inclusion composition is shown in Table 3, and Yttrium base rare earth strand complex inclusion pattern is shown in Fig. 2, Fig. 3.Fig. 2 gets the bid J48-1, J48-2 in numbers 1,2 correspondence tables 3, J48-3, J48-4 in the correspondence of label 3,4 table 3 in Fig. 3.At correspondence steel plate thickness 1/2 Laterally, sampling impact fracture Yttrium base rare earth complex inclusion composition in longitudinal direction is shown in Table 4, and Yttrium base rare earth steel plate is horizontal, impact of collision is broken Mouth complex inclusion pattern is shown in Fig. 4, Fig. 5, and in Fig. 4, label 1,2 corresponds to horizontal sample H-1/2-1, H-1/2-2 in table 4, in Fig. 5 Longitudinal test piece Z-1/2-1, Z-1/2-2 in the correspondence table 4 of label 1,2.
2 Yttrium base rare earth of table processes steel CCSEH36 strand compositions, wt%
Heat (batch) number C Mn Si P S Cr Alt V Nb Cu N Ti Y Ce Remarks
J48 0.13 1.20 0.21 0.021 0.003 0.07 0.023 0.003 0.017 0.05 0.0065 0.011 0.006 0.023 Head 1
J48 0.11 1.24 0.23 0.019 0.003 0.07 0.023 0.004 0.021 0.04 0.007 0.011 0.006 0.023 Afterbody 1
J48 0.10 1.27 0.24 0.019 0.002 0.07 0.023 0.004 0.024 0.04 0.0072 0.011 0.006 0.023 Head 2
From table 2 it can be seen that Yttrium base rare earth processes the Ce containing 0.006% Y and 0.023% in steel strand composition, rise Microalloying Effect, refines matrix.By to Yttrium base rare earth strand complex inclusion composition detection, with reference to table 3, Fig. 2, figure 3, it can be seen that in steel, sulfide, oxide, oxysulfide are mingled with and are caught by Yttrium base rare earth, and form small and dispersed with yttrium is Main Yttrium base rare earth complex inclusion form.
3 Yttrium base rare earth of table processes Yttrium base rare earth complex inclusion composition at steel CCSEH36 slab thicknesses 1/4
Test point Element O Mg Al Y Ce Ca S Fe Field trash
J48-1 Wt% -- -- -- -- -- 57.59 42.41 -- Calcium sulfide
J48-2 Wt% 18.43 -- -- 66.71 13.77 1.09 -- -- Oxide
J48-3 Wt% 23.36 0.97 5.43 45.21 13.73 10.06 -- 1.24 Oxide
J48-4 Wt% 20.68 4.47 8.72 27.62 3.50 24.86 8.98 1.17 Oxysulfide
4 Yttrium base rare earth of table processes steel CCSEH36 steel plate transverse and longitudinal impact fracture Yttrium base rare earth complex inclusion compositions
Test point Element O Mg Al Y Ce S Ca Fe
H-1/2-1 Wt% 10.60 1.41 -- 25.72 14.39 12.28 1.31 34.29
H-1/2-2 Wt% 8.51 -- -- 30.34 13.32 17.69 2.10 28.04
Z-1/2-1 Wt% 9.66 -- -- 33.30 11.08 8.63 -- 37.33
Z-1/2-2 Wt% 12.25 -- -- 29.33 9.68 12.59 2.48 33.67
With reference to table 4, Fig. 4, Fig. 5, it can be seen that steel inclusion is combined for the Yttrium base rare earth based on yttrium of small and dispersed Field trash.
Other cases：Heat (batch) number J51 Yttrium base rare earths are processed at steel slab thickness 1/2 or Yttrium base rare earth complex inclusion at 1/4 Composition is shown in Table 5, and correspondence Yttrium base rare earth processes steel steel plate transverse and longitudinal impact fracture Yttrium base rare earth complex inclusion composition and is shown in Table 6.
5 Yttrium base rare earth of table is processed at steel slab thickness 1/2 or Yttrium base rare earth complex inclusion composition at 1/4
Test point Element O Mg Al Y Ce Ca S Fe Field trash
J51-1/2-1 Wt% -- -- -- -- -- 42.58 57.42 -- Calcium sulfide
J51-1/2-2 Wt% 20.38 -- -- 69.15 10.47 -- -- -- Oxide
J51-1/4-1 Wt% 19.71 -- -- 65.68 13.55 1.06 -- -- Oxide
J51-1/4-2 Wt% 17.83 -- -- 62.18 14.38 1.51 2.43 1.67 Oxysulfide
6 Yttrium base rare earth of table processes steel steel plate transverse and longitudinal impact fracture Yttrium base rare earth complex inclusion composition
Test point Element O Mg Al Y Ce S Ca Fe
J55-H-1/4-1 Wt% 11.25 0.58 -- 48.74 4.10 7.40 2.26 25.67
J55-H-1/4-2 Wt% 17.16 -- -- 39.99 10.24 13.52 2.85 16.24
J55-Z-1/2-1 Wt% 17.46 -- -- 32.41 15.33 10.98 1.14 22.68
J55-Z-1/2-2 Wt% 10.52 -- -- 52.18 12.72 8.08 0.91 15.59
In order to verify the technology of the present invention effect, CCSEH36 high-strength ship plates are carried out with addition Yttrium base rare earth and has not been added Plus Yttrium base rare earth contrast test, sampling at steel plate thickness 1/4, impact property testing result is shown in Table 7, -80 DEG C of horizontal, longitudinal direction punchings Hit fracture apperance contrast and see Fig. 6, Fig. 7, Fig. 8, Fig. 9.
Table 7 is containing Yttrium base rare earth and the impact property testing result without Yttrium base rare earth CCSEH36 steel plates
As can be seen from Table 7, without Yttrium base rare earth steel plate impact property as impact temperature is reduced, the range of decrease under impact property Degree becomes worse and worse, especially side knock performance than larger.And contain Yttrium base rare earth steel plate impact hydraulic performance decline than shallower, Less, longitudinal impact property is maintained at more than 177J to amplitude, and side knock property retention is in more than 103J, and transverse and longitudinal difference Diminish, illustrate to add the low temperature impact properties that Yttrium base rare earth substantially improves steel plate.- 80 DEG C are shown from Fig. 6, Fig. 7, Fig. 8, Fig. 9 Laterally, impact of collision fracture apperance is contrasted it can also be seen that under -80 DEG C of cryogenic conditions, Fig. 6, Fig. 7 show steel containing Yttrium base rare earth Impact fracture pattern is improve in dimple with the presence of many tiny dimples, the Yttrium base rare earth complex inclusion of small and dispersed Shock resistance.And Fig. 8, Fig. 9 show, side knock energy absorption is illustrated The limit has been arrived in 22.9J steel plates shock resistance.
According to 2 produced P460NL2 high-strength pressure vessels plate example strand of technical scheme into table 8 is respectively in, in steel plate Sample at thickness 1/4, contrast impact property testing result is shown in Table 9.
8 Yttrium base rare earth of table processes steel P460NL2 strand compositions, wt%
Heat (batch) number C Mn Si P S Cr Ni Cu Mo V Ti Alt Nb N Y Ce
J137 0.17 1.61 0.38 0.007 0.002 0.04 0.32 0.06 0.005 0.160 0.003 0.006 0.001 0.011 0.009 0.020
J138 0.18 1.65 0.34 0.006 0.002 0.05 0.31 0.05 0.004 0.162 0.002 0.007 0.002 0.010 0.010 0.025
J139 0.16 1.56 0.43 0.005 0.001 0.03 0.34 0.06 0.005 0.168 0.006 0.006 0.001 0.009 0.008 0.018
J140 0.19 1.38 0.40 0.005 0.003 0.03 0.33 0.05 0.005 0.146 0.002 0.008 0.001 0.008 0.007 0.022
Table 9 is containing Yttrium base rare earth and the impact property testing result without Yttrium base rare earth P460NL2 steel plates
As can be seen from Table 9, it is also to reduce with impact temperature without Yttrium base rare earth steel plate impact property, impact property is big Amplitude declines, and becomes worse and worse, especially side knock performance.And contain Yttrium base rare earth steel plate impact hydraulic performance decline than shallower, Less, longitudinal impact property is maintained at more than 135J to amplitude, and in more than 107J, yttrium is added in same explanation for side knock property retention Base rare earth substantially improves the low temperature impact properties of steel plate.
Final statement：The scope of the present invention is not limited thereto, technology according to the present invention scheme and its inventive concept Equivalent or change in addition, should all be included within the scope of the present invention.

Claims (1)

1. a kind of manufacture method of the high-strength steel sheet for being exclusively used in improving low-temperature impact toughness, its processing step：
1）, converter smelting：Smelted using top and bottom complex blowing oxygen coverter, the deoxidation alloying in tapping process, oxygen content control System is in 32 ~ 68ppm；
2）, LF stove refines：After molten steel enters refine station, argon bottom-blowing, while Calx, refining slag and submerged arc slag are added, then It is powered and heats up, after heating up 8 minutes, thermometric, sampling carry out trimming, while according to the situation of top slag, adds carbide and aluminum shot Make white slag, the white slag retention time is more than 15 minutes, then carry out thermometric, sampling again, finely tune alloying component, treat liquid steel temperature, After composition is up to standard, calcium line is fed, after 1～2 minute, then with the speed feeding Yttrium base rare earth silicon calcium alloy claded wire of 2～3m/s 300m～500m, line feeding carry out soft blow argon after terminating, soft argon blowing time 8～15 minutes promotes field trash fully to float and enters molten Slag, obtains molten steel composition its mass percent in following scope：C：0.07% ~ 0.19%, Si：0.15% ~ 0.45%, Mn：1.15%~ 1.65%, P≤0.025%, S≤0.008%, Nb≤0.04%, V≤0.20%, Ti≤0.015%, Ni≤0.40%, Cr≤ 0.10%, Cu≤0.10%, Mo≤0.08%, Alt：0.005% ~ 0.030%, N≤0.020%, O：0.002% ~ 0.003%, it is solid in steel Molten Y：0.005% ~ 0.010%, solid solution Ce：0.015%~0.025%；Field trash is remained in steel shape is combined with O, Mg, Al, S with Y, Ce Complex inclusion form into small and dispersed is present, and in the complex inclusion component comprising Y, Ce mass percent is：Y： 25.72% ~ 69.15%, Ce：3.09%~17.52%；Its balance of ferrum Fe and inevitable impurity；
3）, continuous casting：Refine terminates, and molten steel is sent to continuous casting workshop carries out being casting continuously to form slab, tundish temperature 1515 DEG C～1540 DEG C, in 0.72 ~ 0.90m/min, secondary cooling water adopts weak cold, air-water spraying cooling to slab casting speed control；
4）, heating cycle：Continuous casting billet is heated to into 1215 ~ 1236 DEG C in heating furnace, heating total time presses 1.15 ~ 1.25 points Clock/mm controls, temperature retention time >=185min；
5）, rolling mill practice：Rolled using two-stage control, start rolling temperature >=1060 DEG C of recrystallization zone rolling, recrystallization zone rolls Make every time reduction ratio to control 28% ~ 38%, middle base treats temperature on roller-way, the start rolling temperature of Unhydrated cement rolling 840～ 880 DEG C, 808～838 DEG C of finishing temperature, the accumulative reduction ratio of Unhydrated cement are controlled 58% ~ 68%；
6）, roller repairing technique：Using stacking slow cooling is concentrated after hot-rolled steel plate, its matrix is tiny ferrite+pearly-lustre Body is organized, and in steel plate, field trash is present with the complex inclusion form that Y, Ce and O, Mg, Al, S combine to form small and dispersed.
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Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2008174776A (en) * 2007-01-17 2008-07-31 Nippon Steel Corp High-strength cold-rolled steel sheet excellent in stretch-flange formability and impact energy absorption characteristic and its production method
JP2009091653A (en) * 2007-09-19 2009-04-30 Jfe Steel Kk High strength welded steel pipe for low temperature use having excellent weld heat affected zone toughness, and its production method
CN102119236A (en) * 2009-10-28 2011-07-06 新日本制铁株式会社 Steel plate for line pipes with excellent strength and ductility and process for production of same
CN102892910A (en) * 2010-05-10 2013-01-23 新日铁住金株式会社 High-strength steel sheet and method for producing same
WO2013089156A1 (en) * 2011-12-15 2013-06-20 新日鐵住金株式会社 High-strength h-section steel with excellent low temperature toughness, and manufacturing method thereof
CN104487601A (en) * 2012-09-11 2015-04-01 株式会社神户制钢所 High-tensile-strength steel plate with excellent low -temperature toughness and manufacturing process therefor
CN104831165A (en) * 2015-04-15 2015-08-12 武汉钢铁(集团)公司 Good low-temperature high-toughness normalizing type high-strength pressure container steel plate and manufacturing method thereof

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2008174776A (en) * 2007-01-17 2008-07-31 Nippon Steel Corp High-strength cold-rolled steel sheet excellent in stretch-flange formability and impact energy absorption characteristic and its production method
JP2009091653A (en) * 2007-09-19 2009-04-30 Jfe Steel Kk High strength welded steel pipe for low temperature use having excellent weld heat affected zone toughness, and its production method
CN102119236A (en) * 2009-10-28 2011-07-06 新日本制铁株式会社 Steel plate for line pipes with excellent strength and ductility and process for production of same
CN102892910A (en) * 2010-05-10 2013-01-23 新日铁住金株式会社 High-strength steel sheet and method for producing same
WO2013089156A1 (en) * 2011-12-15 2013-06-20 新日鐵住金株式会社 High-strength h-section steel with excellent low temperature toughness, and manufacturing method thereof
CN104487601A (en) * 2012-09-11 2015-04-01 株式会社神户制钢所 High-tensile-strength steel plate with excellent low -temperature toughness and manufacturing process therefor
CN104831165A (en) * 2015-04-15 2015-08-12 武汉钢铁(集团)公司 Good low-temperature high-toughness normalizing type high-strength pressure container steel plate and manufacturing method thereof

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2021091138A1 (en) * 2019-11-04 2021-05-14 주식회사 포스코 Steel plate having high strength and excellent low-temperature impact toughness and method for manufacturing thereof

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