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WO2018117678A1 - Matériau en acier austénitique présentant de remarquabes caractéristiques de surface, et son procédé de production - Google Patents

Matériau en acier austénitique présentant de remarquabes caractéristiques de surface, et son procédé de production Download PDF

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Publication number
WO2018117678A1
WO2018117678A1 PCT/KR2017/015215 KR2017015215W WO2018117678A1 WO 2018117678 A1 WO2018117678 A1 WO 2018117678A1 KR 2017015215 W KR2017015215 W KR 2017015215W WO 2018117678 A1 WO2018117678 A1 WO 2018117678A1
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steel
excluding
carbide
cooling
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Ceased
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English (en)
Korean (ko)
Inventor
김용진
오홍열
강상덕
이운해
하유미
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Posco Holdings Inc
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Posco Co Ltd
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Priority to US16/471,777 priority Critical patent/US20200087751A1/en
Priority to EP17884959.2A priority patent/EP3561122A4/fr
Priority to JP2019534166A priority patent/JP2020509211A/ja
Priority to CN201780079005.XA priority patent/CN110088343A/zh
Priority to CA3047237A priority patent/CA3047237A1/fr
Publication of WO2018117678A1 publication Critical patent/WO2018117678A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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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
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • 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
    • C21D8/0247—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
    • 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
    • C22C38/06—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • 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
    • C21D2211/001—Austenite
    • 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
    • C21D2211/004—Dispersions; Precipitations

Definitions

  • the present invention provides an austenitic steel having excellent abrasion resistance for use in mining, transportation, and storage in oil and gas industries, such as industrial machinery, structural materials, steel for slurry pipes, and sour steels.
  • the present invention relates to an austenitic steel having excellent surface properties having excellent wear resistance, toughness, corrosion resistance, and the like, and a manufacturing method thereof.
  • Austenitic steels are used for various purposes due to their properties such as work hardening and nonmagnetic properties. Particularly, as carbon steel mainly composed of ferrite or martensite, which is mainly used, exhibits limitations in its characteristics, its application is increasing as an alternative material to overcome these disadvantages.
  • Hadfield steel has been widely used as a wear-resistant component in various industries for its excellent wear resistance, and efforts to increase austenite structure and abrasion resistance by containing a high amount of carbon and containing a large amount of manganese have been made to increase wear resistance of steel materials. It has been a steady progress.
  • the high carbon content of the headfield steel produces network-shaped carbides along the austenite grain boundaries at high temperatures, which drastically lowers the properties, particularly ductility, of the steels.
  • a method of manufacturing high manganese steel by quenching heat treatment or solution treatment at high temperature and quenching to room temperature after hot working has been proposed.
  • the hard field steel has excellent wear resistance in general mechanical wear environments, but it is difficult to show excellent wear resistance in environments accompanied with corrosion wear, and thus it is difficult to apply to harsh environments where complex wear occurs.
  • austenitic wear resistant steels have been developed to secure corrosion resistance.
  • toughness deterioration due to carbide precipitation is always a problem in austenitic wear resistant steels having a very high carbon content, and ingot or cast steel of high manganese steel inevitably segregates due to alloying elements such as manganese and carbon during solidification. This is further worsened during post-processing such as hot rolling, which eventually results in partial precipitation of carbides along the segregation zone in the final product in the form of a network, which in turn promotes non-uniformity of microstructure and deteriorates physical properties. Therefore, in the austenitic wear-resistant steel, research has been mainly made to prevent physical deterioration due to carbide precipitation.
  • Another problem is the non-uniform oxidation that occurs on the surface, and this non-uniform oxidation occurs especially along the grain boundaries, causing cracks in the slab reheating process, growing cracks in the stress rolling process, and improving the surface characteristics of the final product. Makes you inferior Cracks on the surface can cause premature fractures during product bending or tensioning, and can reduce wear resistance.
  • Patent Document 1 Korean Patent Publication No. 2010-0106649
  • One preferred aspect of the present invention is to provide an austenitic steel having excellent surface properties by suppressing heterogeneous oxidation to improve surface quality.
  • Another preferred aspect of the present invention is to provide a method for producing an austenitic steel having excellent surface properties by improving the surface quality by inhibiting heterogeneous oxidation.
  • the microstructure consists of% by area, less than 5% of carbide and residual austenite tissue Austenitic steels having excellent surface properties having a surface defect size of 0.3 mm or less are provided.
  • a method for producing an austenitic steel having excellent surface properties including a cooling step of cooling the hot rolled steel to 600 ° C or lower at a cooling rate of 5 ° C / s or more.
  • the inventors of the present invention while studying the steel having excellent strength and wear resistance compared to the existing steel used in the technical field requiring wear resistance, in the case of high manganese steel can not only secure the excellent strength and elongation peculiar to the austenitic steel, In the case of improving the work hardening rate, the work hardening of the material itself in the abrasion environment, the hardness is rather high, thereby recognizing that excellent wear resistance can be obtained, and thus, the present invention has been completed.
  • the wear-resistant steel having excellent surface properties as well as wear resistance by deriving the reheating conditions of the slab before hot rolling to suppress heterogeneous oxidation. It has been recognized that can be prepared.
  • Austenitic steels having excellent surface properties according to a preferred aspect of the present invention, in weight%, carbon (C): 0.6-1.3%, manganese (Mn): 14-22%, copper (Cu): 5% or less (Excluding 0%), chromium (Cr): 5% or less (excluding 0%), silicon (Si): 1.0% or less (excluding 0%), aluminum (Al): 0.5% or less (excluding 0%), phosphorus ( P): less than 0.1% (including 0%), sulfur (S): less than 0.02% (including 0%), containing the remaining iron (Fe) and other unavoidable impurities; It is composed of carbide and residual austenite structure, and the surface defect size is less than 0.3mm.
  • Carbon (C) is an austenite stabilizing element that not only plays a role of improving the uniform elongation, but is also an element that is very advantageous for improving the strength and the work hardening rate. If the carbon content is less than 0.6%, it may be difficult to form stable austenite at room temperature, and it may be difficult to secure sufficient strength and work hardening rate. On the other hand, when the content exceeds 1.3%, carbides are precipitated in large quantities, thereby reducing the uniform elongation, which may make it difficult to obtain excellent elongation, leading to abrasion resistance decline and premature fracture.
  • the C content is preferably limited to 0.6 to 1.3%.
  • More preferred content of C may be 0.6 to 1.25%.
  • Manganese (Mn) is a very important element that plays a role of stabilizing austenite, and improves uniform elongation.
  • Mn is included in 14% or more.
  • the austenite stability may be lowered to form martensite structure, which may make it difficult to secure sufficient uniform elongation if the austenite structure is not sufficiently secured.
  • the content exceeds 22%, not only the manufacturing cost increases, but also there are problems such as deterioration of corrosion resistance due to manganese addition and difficulty in manufacturing process.
  • the Mn content is preferably limited to 14-22%.
  • Cu copper
  • Cu copper
  • the upper limit is preferably limited to 5%.
  • the content of copper for obtaining the above-mentioned carbide suppression effect it is more preferable that it is 0.05% or more.
  • Even more preferred content of Cu may be 0.05-3.0%.
  • Chromium is dissolved in austenite up to the range of the proper amount of addition, and serves to increase the strength of the steel. Chromium is also an element that improves the corrosion resistance of steels.
  • chromium is a carbide element, in particular, an element that reduces the toughness by forming carbide at the austenite grain boundary. Therefore, it is preferable to determine the content of chromium added in the present invention paying attention to the relationship between carbon and other elements added together, and in order to prevent carbide formation, the upper limit of the Cr content is preferably limited to 5%. . When the Cr content exceeds 5%, it is difficult to effectively suppress the formation of chromium carbide at the austenite grain boundary, and thus there is a problem that the impact toughness is reduced. Therefore, the chromium content is preferably limited to 5% or less.
  • Aluminum (Al), silicon (Si) is a component included as a deoxidizer during the steelmaking process
  • the steel material of the present invention may include aluminum (Al), silicon (Si) within the above limited component range.
  • Phosphorus (P) and sulfur (S) are representative impurities, and it is preferable to limit the phosphorus (P) to 0.1% or less and sulfur (S) to 0.02% or less because they may cause quality deterioration when excessively added.
  • the remaining components of the present invention are iron (Fe) and other unavoidable impurities.
  • iron Fe
  • impurities that are not intended from the raw material or the surrounding environment may be inevitably mixed, and thus cannot be excluded.
  • the austenitic steel according to one preferred aspect of the present invention has a microstructure consisting of carbide and residual austenite structure of 5% or less in area%, and the size of surface defects is 0.3 mm or less. More preferably, the size of the surface defects is 0.2 mm or less.
  • the carbide When the content of the carbide exceeds 5%, the carbide surrounds the grain boundary, which may cause the elongation and impact toughness to drop sharply.
  • the size of the surface defects presented can be defined as, for example, the length from the point where the crack starts to the point where it stops.
  • a method for producing an austenitic steel having excellent surface properties is% by weight, carbon (C): 0.6 to 1.3%, manganese (Mn): 14 to 22%, and copper (Cu): 5% or less (except 0%), chromium (Cr): 5% or less (except 0%), silicon (Si): 1.0% or less (except 0%), aluminum (Al): 0.5% or less (except 0%) Phosphorus (P): 0.1% or less (including 0%), Sulfur (S): 0.02% or less (including 0%), steel slab containing the remaining iron (Fe) and other unavoidable impurities Reheating slab in the reheating step;
  • Hot rolling to obtain a hot rolled steel by hot rolling the heated slab to a finish rolling temperature of 850 to 950 ° C .;
  • It comprises a cooling step of cooling the hot rolled steel to 600 ° C or less at a cooling rate of 5 ° C / s or more.
  • the slabs Prior to hot rolling, the slabs are reheated at 1000 ° C. to 1150 ° C. It is necessary to reheat above 1000 °C to secure sufficient temperature during hot rolling, and to reheat below 1150 °C to suppress the surface uneven oxidation of high Mn steel slab.
  • the slab reheated as above is hot rolled to obtain a finish rolling temperature of 850 to 950 ° C. to obtain a hot rolled steel.
  • the finish rolling temperature is less than 850 °C the carbide may be precipitated to reduce the uniform elongation, the microstructure is pancake may cause uneven stretching due to the anisotropy of the tissue. Meanwhile, When the finish rolling temperature exceeds 950 ° C., the rolling finish temperature is too high, and it is difficult to hit the target temperature in actual process.
  • the hot rolled steel obtained through the hot rolling is cooled to 600 ° C. or less at 5 ° C./s or more.
  • the cooling rate is less than 5 °C / s, or the cooling stop temperature exceeds 600 °C may cause a problem that the carbide is precipitated elongation is lowered. Rapid cooling also helps to ensure high solubility of the C and N elements in the matrix. Therefore, the cooling is preferably carried out to 5 °C / s or more to 600 °C or less.
  • the cooling rate is more preferably at a rate of 10 ° C / s or more, and even more preferably at a rate of 15 ° C / s or more.
  • the slab satisfying the component system and composition range as shown in Table 1 was prepared as a hot rolled steel sheet having a thickness of 12mm through the reheating and rolling conditions shown in Table 2.
  • the invention steel (1-4) satisfies both the component range and the manufacturing conditions, the invention steel (1-4) all show good surface properties.
  • the comparative steel (1) shows that C is very low and thus does not secure sufficient strength.
  • Comparative steel (2) shows that carbides increase due to excessive C addition, and elongation and impact toughness drop sharply.
  • Comparative steel (4) shows that the elongation and impact toughness plummet due to excessive carbide formation when the Cr content is exceeded.
  • Comparative steel 5 shows that a large defect occurred on the surface of the product because the reheating temperature exceeded the reference value.
  • Comparative steel 6-8 shows that the toughness of the rolling finish temperature, cooling rate, cooling stop temperature, etc. falls outside the scope of the present invention and the impact toughness drops sharply due to excessive precipitation of carbides.
  • the comparative steel (5) having a high reheating temperature has a large crack formed on the surface, in the case of the invention steel (3) to which the low temperature reheating temperature is applied, the surface layer is uniform, there is no large crack can confirm.

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

Abstract

La présente invention concerne un matériau en acier austénitique résistant à l'abrasion présentant de remarquables caractéristiques de surface, et un procédé de production de ce matériau en acier austénitique résistant à l'abrasion. L'invention concerne un matériau en acier austénitique présentant de remarquables caractéristiques de surface, et son procédé de production, le matériau en acier austénitique selon la présente invention comprenant, en % massiques : 0,6 à 1,3 % de carbone (C) ; 14 à 22 % de manganèse (Mn) ; 5 % ou moins (à l'exclusion de 0 %) de cuivre (Cu) ; 5 % ou moins (à l'exclusion de 0 %) de chrome (Cr) ; 1,0 % ou moins (à l'exclusion de 0 %) de silicium (Si) ; 0,5 % ou moins (à l'exclusion de 0 %) d'aluminium (Al) ; 0,1 % ou moins (y compris 0 %) de phosphore (P) ; 0,02 % ou moins (y compris 0 %) de soufre (S) ; le reste étant constitué de fer (Fe) et d'autres impuretés inévitables. Ce matériau présente une microstructure comprenant, en % en surface, 5 % ou moins de carbure, le reste correspondant à la structure austénitique, et une taille des défauts superficiels de 0,3 mm ou moins.
PCT/KR2017/015215 2016-12-23 2017-12-21 Matériau en acier austénitique présentant de remarquabes caractéristiques de surface, et son procédé de production Ceased WO2018117678A1 (fr)

Priority Applications (5)

Application Number Priority Date Filing Date Title
US16/471,777 US20200087751A1 (en) 2016-12-23 2017-12-21 Austenitic steel having excellent surface characteristics, and method of manufacturing the same
EP17884959.2A EP3561122A4 (fr) 2016-12-23 2017-12-21 Matériau en acier austénitique présentant de remarquabes caractéristiques de surface, et son procédé de production
JP2019534166A JP2020509211A (ja) 2016-12-23 2017-12-21 表面特性に優れたオーステナイト系鋼材及びその製造方法
CN201780079005.XA CN110088343A (zh) 2016-12-23 2017-12-21 具有优异表面特性的奥氏体钢及其制造方法
CA3047237A CA3047237A1 (fr) 2016-12-23 2017-12-21 Materiau en acier austenitique presentant de remarquabes caracteristiques de surface, et son procede de production

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
KR10-2016-0178238 2016-12-23
KR1020160178238A KR101920973B1 (ko) 2016-12-23 2016-12-23 표면 특성이 우수한 오스테나이트계 강재 및 그 제조방법

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WO2018117678A1 true WO2018117678A1 (fr) 2018-06-28

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US (1) US20200087751A1 (fr)
EP (1) EP3561122A4 (fr)
JP (1) JP2020509211A (fr)
KR (1) KR101920973B1 (fr)
CN (1) CN110088343A (fr)
CA (1) CA3047237A1 (fr)
WO (1) WO2018117678A1 (fr)

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WO2021167332A1 (fr) * 2020-02-18 2021-08-26 주식회사 포스코 Tôle d'acier ayant une excellente qualité de surface, et son procédé de fabrication
WO2022139396A1 (fr) * 2020-12-21 2022-06-30 주식회사 포스코 Acier austénitique à haute teneur en manganèse pour frein à disque
CN114015942B (zh) * 2021-11-04 2022-07-29 广东美芝制冷设备有限公司 无磁平衡块及其制备方法、压缩机
CN119278290A (zh) * 2022-06-02 2025-01-07 安赛乐米塔尔公司 高锰热轧钢及其生产方法

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US20200087751A1 (en) 2020-03-19
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EP3561122A1 (fr) 2019-10-30
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