WO2013095005A1 - Feuille d'acier à haute teneur en manganèse, non magnétique, ayant une haute résistance et son procédé de fabrication - Google Patents

Feuille d'acier à haute teneur en manganèse, non magnétique, ayant une haute résistance et son procédé de fabrication Download PDF

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Publication number
WO2013095005A1
WO2013095005A1 PCT/KR2012/011168 KR2012011168W WO2013095005A1 WO 2013095005 A1 WO2013095005 A1 WO 2013095005A1 KR 2012011168 W KR2012011168 W KR 2012011168W WO 2013095005 A1 WO2013095005 A1 WO 2013095005A1
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WO
WIPO (PCT)
Prior art keywords
steel sheet
less
high strength
manganese steel
magnetic
Prior art date
Application number
PCT/KR2012/011168
Other languages
English (en)
Korean (ko)
Inventor
김성규
진광근
오필용
황현규
Original Assignee
주식회사 포스코
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority claimed from KR1020110141738A external-priority patent/KR20130073736A/ko
Priority claimed from KR1020110142433A external-priority patent/KR20130074384A/ko
Application filed by 주식회사 포스코 filed Critical 주식회사 포스코
Priority to JP2014548662A priority Critical patent/JP6002779B2/ja
Priority to US14/367,480 priority patent/US20150211088A1/en
Priority to EP12859366.2A priority patent/EP2796585B1/fr
Priority to CN201280064011.5A priority patent/CN104011248B/zh
Publication of WO2013095005A1 publication Critical patent/WO2013095005A1/fr

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Classifications

    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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
    • 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
    • C21D8/0236—Cold rolling
    • 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
    • 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
    • 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
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium

Definitions

  • the present invention relates to a high-strength high manganese steel sheet having nonmagnetic properties that can be used for an electric power generator such as a switchboard and a transformer.
  • Ferritic or martensitic stainless steel may be used to increase the strength, but since the ferritic or martensitic stainless steel has high magnetic properties, not only does power loss due to eddy currents occur, but the price is very expensive. have.
  • One aspect of the present invention is to provide a high-strength high manganese steel sheet and a method for manufacturing the same having excellent strength and formability, as well as excellent nonmagnetic properties.
  • the austenitic stability is increased to secure nonmagnetic properties, and A1 or the like is added to prevent carbon from forming carbides, thereby providing a high manganese steel which makes austenite more stable. It has the advantage of excellent moldability. Thus, it provides sufficient rigidity for use as structural members such as large transformers.
  • Figure 1 (a) is a photograph of observing the microstructure of Inventive Example 1-7 and (b) Comparative Example 1-4.
  • 2 (a) and 2 (b) are XRD graphs measuring the degree of image stability of Inventive Steel 2-1 and Comparative Steel 2-1, respectively.
  • FIG. 3 are photographs of the microstructures of the inventive steels 2-1 and Comparative steels 2-1, respectively. Best Mode for Implementation of the Invention
  • the loss due to the eddy currents of the material exposed to the electromagnetic field is closely related to the magnetism of the material.
  • magnetism is proportional to permeability ( ⁇ ).
  • the present inventors have studied in depth, and in order to have high strength and nonmagnetic properties, the inventors have invented high manganese steel having high austenite stability by adding manganese (Mn) and carbon (C) to steel.
  • Mn manganese
  • C carbon
  • the austenite phase stability is increased, and the addition of aluminium suppresses the slip deformation due to the formation and dislocation of ⁇ -martensite during deformation, thereby providing excellent strength and elongation (formability).
  • the present invention will be described in detail.
  • the steel sheet of the present invention satisfies the following composition (hereinafter increased%) Carbon (C): 0.4-0.9%
  • Mn Manganese
  • Mn is an important element that plays a role in stabilizing austenite tissue and contains 10% or more in the present invention. If it is less than 10%, ⁇ '-martensite phase is present, and the nonmagnetic property is deteriorated. If it is more than 25%, manufacturing atoms are greatly increased. There is a problem of deterioration. Therefore, the content of Mn is preferably 10-25%.
  • the A1 is an element effective to prevent the formation of carbides, and improves formability by adjusting the fraction of twins.
  • carbon is contained in an amount of 0.01% or more because it acts as an important element to prevent carbide formation in order to stabilize the austenite and improve nonmagnetic properties.
  • it exceeds 8.03 ⁇ 4 the manufacturing cost increases, and the surface quality of the product is lowered due to the formation of excessive ⁇ oxide, so that the content is preferably 0.01-8.0%.
  • the Si is an element that does not significantly affect the lamination defect energy, and is usually used as a deoxidizer or contained in a general steelmaking process, and if it is to be removed, it contains 0.01% because excessive cost occurs, If the content exceeds 2.0%, the manufacturing cost increases, and the surface quality of the product is reduced due to the formation of excessive oxide, the content is preferably 0.01-2.0%. Titanium (Ti): 0.05-0.2%
  • the Ti is added to ensure strength and formability as a component that reacts with nitrogen inside the steel to precipitate nitride and form twins.
  • the Ti forms a precipitated phase to increase the strength.
  • Ti is small to wind contained 0.05% or more, but if it exceeds 0 .23 ⁇ 4 are formed to precipitate the excess can be a micro-cracks formed during cold rolling, can lead to deterioration of the formability and weldability. Therefore, the content of Ti is preferably 0.05 to 0.2%.
  • the S needs to be controlled to 0.05% or less for the control of inclusions.
  • the upper limit thereof is preferably 0.05%.
  • P is an element that segregation easily occurs to promote cracking during casting. In order to prevent this, it is preferable to control to 0.8% or less. If the content of P exceeds 0.8%, castability may deteriorate, so the upper limit is 0.8%. desirable .
  • N is an element which is indispensably added to the atmosphere during the steelmaking process. Reducing the N to less than 0.003% is an excessive cost in the process, when the content is more than 0.01% because it forms a nitride to lower the formability, it is not preferable. Therefore, the content of N is preferably 0.003-0.01%. The remainder contains Fe and inevitable impurities.
  • carbides are contained in the microstructure of 1% by volume or less.
  • carbon must be dissolved in an atomic state, thereby securing austenite stability. In other words, when carbon is present in steel in the form of carbides, the austenite has low stability, high permeability, and inferior magnetic properties.
  • the number of steels and carbides is as small as possible, and it is desirable to form one volume 3 ⁇ 4 or less.
  • the carbide is preferably included in less than 1% by volume even after the heat treatment.
  • the heat treatment includes not only heat treatment existing in the manufacturing process of the steel sheet, but also heat treatment performed in the process of using the steel pipe.
  • the steel sheet of the present invention has an austenite structure, in order to maintain the austenite structure in order to maintain nonmagnetic in external energy such as heat treatment. Therefore, the steel sheet of the present invention has an austenite structure, and it is preferable that carbides are formed in part (1% by volume or less) depending on the heat treatment conditions.
  • the stacking fault energy (SFE) value is preferably 30 mJ / ciif or more.
  • the lamination defect energy is an energy of an interface between partial potentials formed in the material, and in the present invention, by controlling the content of A1, the lamination defect is controlled, thereby improving the phase stability of the austenite phase. If the stacking defect energy has an appropriate value, the potential and twin are in harmony, and thus the phase stability increases, but if it becomes too low, the potential cannot be generated or moved, and the phase stability decreases. Robbery is done. Therefore, in the present invention, the optimum stacking defect energy is derived to obtain phase stability with moderate strength.
  • the lamination defect energy value is preferably 30 mJ / cuf or more.
  • the method of measuring the stacking defect energy is various, such as X-ray measurement method, transmission electron microscope measurement method, thermodynamic calculation method, etc., thermodynamic calculation method using the thermodynamic data that reflects the influence of the components well, and easy to measure is most preferred.
  • the steel sheet of the present invention has a tensile strength of 800MPa or more, and by securing an elongation of 15% or more, it is desirable to have excellent strength and workability.
  • the heating temperature is too low, it is preferable to heat at a temperature of 1100 ° C. or more because the rolling load may be excessively taken during hot rolling. The higher the degree of heating, the easier the hot rolling. However, the steel with a high content of Mn may cause severe oxidation inside the high-temperature heating yarn, which may lower the surface quality. Therefore, the upper limit of the reheating temperature is preferably 1250 o C. .
  • the hot finish rolling temperature is also easy to roll due to the low deformation resistance at higher temperature, but the higher the rolling degree, the lower the surface quality. Therefore, the temperature is preferably lower than 1000 o C.
  • the temperature is too low. Since it becomes large, it is preferable to carry out at 800 ° C or more.
  • After the hot rolling is subjected to the step of winding. It is preferable to perform the said coiling at 400-700 degreeC .
  • the cooling rate after the said winding is usually slow. If the coiling start temperature is too low, a large amount of cooling water is required for deflection, and the coiling load acts largely so that the coiling start temperature is 400 o C or more.
  • the coiling temperature is preferably 700 ° C. or lower.
  • the hot rolled steel sheet prepared as described above is cold rolled to prepare a molten steel sheet.
  • the rolling reduction during inter rolling is generally determined according to the required thickness of the product.
  • the recrystallization proceeds during the heat treatment after the inter rolling, it is necessary to control the driving force of the recrystallization well. In other words, if the reduction ratio during rolling is too low, the strength of the product is lowered. Therefore, the reduction of the product is performed at a reduction ratio of 30% or more. It is preferable to carry out at a reduction ratio of 60% or less.
  • continuous annealing is performed.
  • the continuous annealing is preferably carried out at 650 ⁇ 900 ° C.
  • Continuous annealing is performed at temperatures above 650 o C where recrystallization occurs It is preferable, but if the annealing temperature is too high, an oxide is formed on the surface, and the peelability with the front / rear connection products which are continuously worked is reduced, so it is preferable to carry out at 900 ° C. or less.
  • VSM records the applied magnetic field applied by the Hall probe, and the magnetization value of the sample is measured by recording the electromotive force obtained when vibrating the sample by Faraday's law. do.
  • VSM is a method of measuring the magnetization value of a sample by detecting the induced electromotive force in the search coil by applying the vibration to the sample by this basic operation and principle.
  • the magnetic properties of the material can be measured simply as a function of magnetic field, temperature and time.
  • the fraction of carbide in the present invention is very small, in the comparative example outside the scope of the present invention it can be seen that the nonmagnetic properties inferior to the fraction of the carbide exceeds 1% by volume. Therefore, it can be seen that excellent nonmagnetic properties can be ensured when the fraction of carbide becomes 1 volume 3 ⁇ 4 or less.
  • Hot finish rolling was performed at 900 ° C., wound at 500 ° C., and then hot-rolled at a rolling reduction rate of 50%, followed by continuous annealing at 800 ° C. to produce a mild steel sheet.
  • Yield strength (YS), tensile strength (TS) and elongation were measured for the ductile steel sheet, and the results are shown in Table 2.
  • SFE stacking fault energy
  • the lamination defect energy (SFE) is 30 mJ / m 2 or more, and the relative permeability is low. That is, it can be seen that excellent nonmagnetic properties can be secured, and that phase stability is high.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)

Abstract

La présente invention concerne une feuille d'acier à haute teneur en manganèse, non magnétique, à haute résistance, qui possède une résistance supérieure et une aptitude au moulage supérieure, et, en même temps, permet d'obtenir des caractéristiques non magnétiques supérieures. L'invention concerne également son procédé de fabrication.
PCT/KR2012/011168 2011-12-23 2012-12-20 Feuille d'acier à haute teneur en manganèse, non magnétique, ayant une haute résistance et son procédé de fabrication WO2013095005A1 (fr)

Priority Applications (4)

Application Number Priority Date Filing Date Title
JP2014548662A JP6002779B2 (ja) 2011-12-23 2012-12-20 非磁性高強度高マンガン鋼板及びその製造方法
US14/367,480 US20150211088A1 (en) 2011-12-23 2012-12-20 Non-magnetic high manganese steel sheet with high strength and manufacturing method thereof
EP12859366.2A EP2796585B1 (fr) 2011-12-23 2012-12-20 Feuille d'acier à haute teneur en manganèse, non magnétique, ayant une haute résistance et son procédé de fabrication
CN201280064011.5A CN104011248B (zh) 2011-12-23 2012-12-20 具有高强度的用于重型电力机械的非磁性高锰钢板及其制造方法

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
KR1020110141738A KR20130073736A (ko) 2011-12-23 2011-12-23 상안정성이 우수한 고강도 비자성 강판과 그 제조방법
KR10-2011-0141738 2011-12-23
KR10-2011-0142433 2011-12-26
KR1020110142433A KR20130074384A (ko) 2011-12-26 2011-12-26 비자성 고강도 고망간 강판 및 그 제조방법

Publications (1)

Publication Number Publication Date
WO2013095005A1 true WO2013095005A1 (fr) 2013-06-27

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PCT/KR2012/011168 WO2013095005A1 (fr) 2011-12-23 2012-12-20 Feuille d'acier à haute teneur en manganèse, non magnétique, ayant une haute résistance et son procédé de fabrication

Country Status (5)

Country Link
US (1) US20150211088A1 (fr)
EP (1) EP2796585B1 (fr)
JP (1) JP6002779B2 (fr)
CN (1) CN104011248B (fr)
WO (1) WO2013095005A1 (fr)

Cited By (2)

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CN104087872A (zh) * 2014-06-24 2014-10-08 宁国市正兴耐磨材料有限公司 一种风扇磨煤机冲击板
EP3061840A4 (fr) * 2013-10-23 2016-10-19 Posco Tôle d'acier à résistance élevée et riche en manganèse ayant d'excellentes propriétés de résistance aux vibrations et son procédé de fabrication

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JP6185865B2 (ja) * 2013-03-21 2017-08-23 株式会社神戸製鋼所 低温曲げ加工性に優れた非磁性鋼およびその製造方法
JP6154768B2 (ja) * 2013-03-21 2017-06-28 株式会社神戸製鋼所 低温曲げ加工性に優れた非磁性鋼
KR101889187B1 (ko) * 2015-12-23 2018-08-16 주식회사 포스코 열간 가공성이 우수한 비자성 강재 및 그 제조방법
KR101747034B1 (ko) 2016-04-28 2017-06-14 주식회사 포스코 항복비가 우수한 초고강도 고연성 강판 및 이의 제조방법
WO2017203315A1 (fr) 2016-05-24 2017-11-30 Arcelormittal Tôle mince en acier laminée à froid et recuite, son procédé de production et utilisation d'un tel acier pour produire des pièces de véhicule
WO2017203311A1 (fr) * 2016-05-24 2017-11-30 Arcelormittal Tôle d'acier laminée à froid et recuite, son procédé de production et utilisation d'un tel acier pour produire des pièces de véhicule
WO2017203310A1 (fr) 2016-05-24 2017-11-30 Arcelormittal Procédé de fabrication d'une tôle d'acier twip à microstructure austénitique
WO2017203312A1 (fr) * 2016-05-24 2017-11-30 Arcelormittal Tôle d'acier laminée à froid et recuite, son procédé de production et utilisation d'un tel acier pour produire des pièces de véhicule
KR101977507B1 (ko) * 2017-12-22 2019-05-10 주식회사 포스코 자기장 차폐용 강판 및 그 제조방법
KR102119962B1 (ko) * 2018-10-25 2020-06-05 주식회사 포스코 용접성이 우수한 고강도 및 고연성 비자성 강재 및 이의 제조방법
KR102255827B1 (ko) * 2018-10-25 2021-05-26 주식회사 포스코 표면품질이 우수한 극저온용 오스테나이트계 고망간 강재 및 그 제조방법
EP3771746A1 (fr) * 2019-08-02 2021-02-03 ThyssenKrupp Steel Europe AG Acier, produit plan en acier, procédé de fabrication d'un produit plan en acier et utilisation
KR102218441B1 (ko) * 2019-10-08 2021-02-19 주식회사 포스코 비자성 고강도 선재 및 이의 제조방법

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CN104011248B (zh) 2016-08-17
US20150211088A1 (en) 2015-07-30
JP6002779B2 (ja) 2016-10-05
EP2796585A1 (fr) 2014-10-29
CN104011248A (zh) 2014-08-27

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