WO2020085855A1 - Acier à haute teneur en manganèse ayant d'excellentes propriétés de coupe à l'oxygène et procédé de fabrication s'y rapportant - Google Patents

Acier à haute teneur en manganèse ayant d'excellentes propriétés de coupe à l'oxygène et procédé de fabrication s'y rapportant Download PDF

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WO2020085855A1
WO2020085855A1 PCT/KR2019/014184 KR2019014184W WO2020085855A1 WO 2020085855 A1 WO2020085855 A1 WO 2020085855A1 KR 2019014184 W KR2019014184 W KR 2019014184W WO 2020085855 A1 WO2020085855 A1 WO 2020085855A1
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cutting
steel
manganese
oxygen
less
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PCT/KR2019/014184
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English (en)
Korean (ko)
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이운해
이동호
조원태
이순기
최창식
강상덕
정영덕
김보성
석정훈
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주식회사 포스코
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Priority claimed from KR1020190118923A external-priority patent/KR102245226B1/ko
Application filed by 주식회사 포스코 filed Critical 주식회사 포스코
Priority to CN201980069176.3A priority Critical patent/CN112912526B/zh
Priority to EP19876472.2A priority patent/EP3872214A4/fr
Publication of WO2020085855A1 publication Critical patent/WO2020085855A1/fr

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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
    • 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
    • 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
    • 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
    • C21D8/0205—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
    • 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
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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

Definitions

  • the present invention relates to a high-manganese steel material and a method for manufacturing the same, and more particularly, to an austenitic high-manganese steel material having excellent oxygen cutting property and a method for manufacturing the same.
  • the austenitic high-manganese steel material is characterized by having high toughness as the austenite is stable even at room temperature by adjusting the content of manganese (Mn) and carbon (C), which are elements that increase the stability of austenite.
  • Austenite is a paramagnetic material with low permeability and excellent non-magnetic properties compared to ferrite. In general, materials used for transformers, switchboards, etc. have a permeability of 1.05 or less, while austenitic high manganese steels have a permeability of 1.02 or less, so it can be seen that they have superior non-magnetic properties compared to conventional materials.
  • austenitic high-manganese steel As a structure, cutting and processing of the material by oxygen cutting are essential, but since high-manganese steel contains a large amount of alloying components, the cutting surface is caused by sparks during oxygen cutting. Heating problems exist. That is, it is not preferable from the viewpoint of productivity because the steel is pre-heated or the cutting speed is adjusted in advance to improve the cutability. Accordingly, there is a need to develop an austenitic high-manganese steel material having economical and effective oxygen cutting processing characteristics.
  • Patent Document 1 Republic of Korea Patent Publication No. 10-2010-0064473 (2010.06.15. Public)
  • a high-manganese steel material having excellent oxygen cutting properties and a method for manufacturing the same can be provided.
  • the high-manganese steel material having excellent oxygen-cutting properties according to an aspect of the present invention, in weight percent, carbon (C): 0.1-0.5%, manganese (Mn): 20-26%, silicon (Si): 0.05-0.4% , Aluminum (Al): 2.0% or less, Chromium (Cr): 4% or less, including residual Fe and other inevitable impurities, and the cutability sensitivity (Sc) calculated by the following [Relational Formula 1] is 430 or more, and 95 area % Or more of austenite.
  • the steel material by weight, may further include 0.0005 to 0.01% boron (B).
  • the magnetic permeability of the steel material may be 1.02 or less.
  • the yield strength of the steel material is 240MPa or more, the tensile strength is 720MPa or more, and the elongation may be 25% or more.
  • the average surface roughness of the steel cutting surface may be 0.5 mm or less.
  • a method of manufacturing a high-manganese steel material having excellent oxygen-cutting properties in weight percent, carbon (C): 0.1-0.5%, manganese (Mn): 20-26%, silicon (Si): 0.05 ⁇ 0.4%, aluminum (Al): 2.0% or less, chromium (Cr): 4% or less, including residual Fe and other unavoidable impurities, and the slab sensitivity (Sc) of 430 or more calculated by [Relational Formula 1] below Re-heating in the temperature range of 1050 ⁇ 1300 °C; Hot rolling the reheated slab to a finish rolling temperature of 800 to 1050 ° C to provide a hot rolled material; And cooling the hot rolled material to a temperature range of 600 ° C. or less at a cooling rate of 1 to 100 ° C./s.
  • the slab by weight, may further include 0.0005 to 0.01% boron (B).
  • an austenitic high-manganese steel material having excellent oxygen cutting properties and a method for manufacturing the same can be provided.
  • FIG. 1 (a) is a photograph of whether a spark is generated during oxygen cutting in Example 2 and a cut surface due to oxygen cutting
  • FIG. 1 (b) shows whether spark is generated during oxygen cutting in Comparative Example 2 and when oxygen is cut. This is a photograph of the cut surface.
  • the present invention relates to a high-manganese steel material having excellent oxygen-cutting properties and a method for manufacturing the same, and the following describes preferred embodiments of the present invention.
  • the embodiments of the present invention may be modified in various forms, and the scope of the present invention should not be construed as being limited to the embodiments described below. These embodiments are provided to those skilled in the art to further detail the present invention.
  • the high-manganese steel material having excellent oxygen-cutting properties according to an aspect of the present invention, in weight percent, carbon (C): 0.1-0.5%, manganese (Mn): 20-26%, silicon (Si): 0.05-0.4% , Aluminum (Al): 2.0% or less, chromium (Cr): 4% or less, the balance may include Fe and other unavoidable impurities.
  • Carbon (C) is an effective element for stabilizing austenite of steel and securing strength by solid solution strengthening, so the present invention can limit the lower limit of the carbon (C) content to a certain range in order to secure low-temperature toughness and strength. .
  • the stability of austenite is insufficient and stable austenite cannot be obtained at room temperature, and it is easily processed into ⁇ -martensite and ⁇ '-martensite by external stress. This is because it can reduce the toughness and strength of the steel. Therefore, the present invention can limit the lower limit of the carbon (C) content to 0.1%.
  • the lower limit of the preferred carbon (C) content is 0.15%, and the lower limit of the more preferred carbon (C) content may be 0.17%.
  • the carbon (C) content exceeds a certain range, the cutting surface may be deteriorated by the occurrence of sparks during oxygen cutting of the steel, or the productivity may be inferior by lowering the cutting speed.
  • the upper limit of can be limited to 0.5%.
  • the upper limit of the preferred carbon (C) content may be 0.47%, and the upper limit of the more preferred carbon (C) content may be 0.45%.
  • Manganese (Mn) is an important element that plays a role in stabilizing austenite, so the present invention can limit the lower limit of the manganese (Mn) content to 20% to achieve this effect. That is, the present invention can effectively increase the austenite stability because it contains 20% or more of manganese (Mn), thereby inhibiting the formation of ferrite, ⁇ -martensite and ⁇ '-martensite, and nonmagnetic properties of steel and It can effectively secure low-temperature toughness.
  • the manganese (Mn) content exceeds a certain level range, the effect of increasing the stability of austenite is saturated, while the manufacturing cost is greatly increased, and surface oxidation may be deteriorated due to excessive internal oxidation during hot rolling.
  • the present invention can limit the upper limit of the manganese (Mn) content to 26%. Therefore, the manganese (Mn) content of the present invention may be 20 to 26%, and a more preferable manganese (Mn) content may be 20 to 24%.
  • Silicon (Si) is an element that is indispensably added in trace amounts as a deoxidizer, such as aluminum (Al).
  • a deoxidizer such as aluminum (Al).
  • the present invention has an upper limit of the silicon (Si) content. It can be limited to 0.4%.
  • the upper limit of the more preferable silicon (Si) content may be 0.3%.
  • an excessive cost is required to reduce the silicon (Si) content in the steel, so the present invention can limit the lower limit of the silicon (Si) content to 0.05%.
  • the lower limit of the more preferable silicon (Si) content may be 0.1%.
  • Aluminum (Al) is a representative element added as a deoxidizer. However, aluminum (Al) may form precipitates by reacting with carbon (C) and nitrogen (N), and the hot workability may be deteriorated by these precipitates, and the present invention provides an upper limit of the aluminum (Al) content. It can be limited to 2.0%.
  • the preferred content of aluminum (Al) may be 0.01 to 2.0%, and the more preferred content of aluminum (Al) may be 0.01 to 1.95%.
  • Chromium (Cr) is a winso that stabilizes austenite up to a range of an appropriate addition amount, thereby contributing to the improvement of non-magnetic properties, and is employed in austenite to increase the strength of steel.
  • chromium (Cr) is also an element that improves the corrosion resistance of steel materials. Therefore, the present invention can add chromium (Cr) to achieve this effect.
  • chromium (Cr) increases the melting temperature of the oxide during oxygen cutting, and as the added content increases, the tendency for oxygen cutting property to deteriorate tends to deteriorate.
  • the upper limit of the chromium (Cr) content is limited to 4%. May be, the upper limit of the more preferred chromium (Cr) content may be 3.5%.
  • the non-magnetic high-manganese steel material having excellent oxygen-cutting properties may include residual Fe and other unavoidable impurities in addition to the above-described components.
  • unintended impurities from the raw material or the surrounding environment may inevitably be mixed, and therefore cannot be entirely excluded. Since these impurities are known to anyone skilled in the art, they are not specifically mentioned in this specification.
  • addition of effective ingredients other than the above composition is not entirely excluded.
  • the high-manganese steel material having excellent oxygen cutting property according to an aspect of the present invention may further include 0.0005 to 0.01% boron (B), and 0.03% or less phosphorus (P), 0.05% It may include one or more of the following sulfur (S) and less than 0.02% nitrogen (N).
  • Boron (B) is a grain boundary strengthening element for strengthening the austenite grain boundary, and is an element capable of effectively lowering the high temperature cracking sensitivity of steel materials by strengthening the austenite grain boundary even with a small amount added. Therefore, in order to achieve this effect, the present invention can limit the lower limit of the boron (B) content to 0.0005%.
  • the lower limit of the more preferred boron (B) content may be 0.001%.
  • the upper limit of the content can be limited to 0.01%.
  • the upper limit of the more preferred boron (B) content may be 0.006%.
  • Phosphorus (P) is not only an element that is inevitably introduced into the steel, but is an element that is easily segregated and causes cracking during casting or degrades weldability. Therefore, the present invention may limit the upper limit of the phosphorus (P) content to 0.03% to prevent deterioration of castability and deterioration of weldability, and the upper limit of the more preferable phosphorus (P) content may be 0.02%.
  • Sulfur (S) is not only an element that is inevitably introduced into the steel, but is also an element that causes hot brittle defects by inclusion formation. Therefore, the present invention can limit the upper limit of the sulfur (S) content to 0.05% to suppress the occurrence of hot embrittlement, the upper limit of the more preferred sulfur (S) content may be 0.02%.
  • Nitrogen (N) is not only an element inevitably introduced into steel, but also an element contributing to solid solution strengthening. However, if the content of nitrogen (N) is excessive, there is a problem of lowering the strength of the steel by forming a coarse nitride, so the present invention can limit the upper limit of the nitrogen (N) content to 0.02%.
  • the cutability sensitivity (Sc) calculated by the following [Relational Formula 1] may be 430 or more. More preferably, the cutting sensitivity (Sc) calculated by the following [Relational Formula 1] may be 460 or more.
  • the inventors of the present invention have conducted an in-depth study in relation to the oxygen-cutting property of high-manganese steel, while aluminum (Al) is an element that positively affects the oxygen-cutting property of high-manganese steel, whereas carbon (C) and manganese (Mn) ) And chromium (Cr) were found to be elements that negatively affect the oxygen-cleavability of high-manganese steels.
  • the inventors of the present invention have conducted a study on the correlation of these carbon (C), manganese (Mn), chromium (Cr), and aluminum (Al) contents, and the sensitivity to cutability (Sc) ) was more than a certain level, it was confirmed that it has excellent oxygen cleavage.
  • the high manganese steel material having excellent oxygen cutting property controls the alloy composition content so that the cutability sensitivity (Sc) by [Relational Formula 1] satisfies 430 or more, so the average of the steel cutting surface during oxygen cutting
  • the surface roughness can be managed at a level of 0.5 mm or less.
  • a high-manganese steel material having excellent oxygen-cutting properties may include at least 95% by area of austenite as a microstructure, thereby effectively securing non-magnetic properties and low-temperature properties of the steel material.
  • the average grain size of austenite may be 5 to 150 ⁇ m.
  • the average grain size of austenite that can be implemented in the manufacturing process is 5 ⁇ m or more, and when the average grain size is greatly increased, the strength of the steel material may be lowered, so the grain size of austenite may be limited to 150 ⁇ m or less.
  • the austenitic high-manganese steel material having excellent oxygen cleavability may include carbide and / or ⁇ -martensite as a structure that may exist in addition to austenite.
  • carbide and / or ⁇ -martensite exceeds a certain level, the toughness and ductility of the steel may be rapidly reduced.
  • the fraction of carbide and / or ⁇ -martensite is less than 5 area%. Can be limited.
  • a high-manganese steel material having excellent oxygen cutting properties according to an aspect of the present invention is provided with an optimal alloy composition, and thus may have an excellent cutting surface during oxygen cutting. That is, since the occurrence of sparks is minimized when oxygen is cut, it is possible to minimize the phenomenon that the cut surface is non-uniform due to melting of the steel material.
  • the high-manganese steel material having excellent oxygen cutting property according to an aspect of the present invention can effectively prevent a decrease in cutting speed when cutting oxygen, thereby optimizing work efficiency and maximizing productivity.
  • a high-manganese steel material having excellent oxygen cutting properties according to an aspect of the present invention may have a permeability of 1.02 or less, a yield strength of 240 MPa or more, a tensile strength of 720 MPa or more, and an elongation of 25% or more.
  • a method of manufacturing a high-manganese steel material having excellent oxygen-cutting properties in weight percent, carbon (C): 0.1-0.5%, manganese (Mn): 20-26%, silicon (Si): 0.05 ⁇ 0.4%, aluminum (Al): 2.0% or less, chromium (Cr): 4% or less, including residual Fe and other unavoidable impurities, and the slab sensitivity (Sc) of 430 or more calculated by [Relational Formula 1] below Re-heating in the temperature range of 1050 ⁇ 1300 °C; Hot rolling the reheated slab to a finish rolling temperature of 800 to 1050 ° C to provide a hot rolled material; And cooling the hot rolled material to a temperature range of 600 ° C. or less at a cooling rate of 1 to 100 ° C./s.
  • the slab by weight, may further include 0.0005 to 0.01% boron (B), 0.03% or less phosphorus (P), 0.05% or less sulfur (S), and 0.02% or less nitrogen (N).
  • B boron
  • P phosphorus
  • S sulfur
  • N nitrogen
  • the description of the steel composition of the slab will be replaced by the description of the steel composition of the steel material described above. do.
  • the slab provided with the above-described steel composition can be reheated in a temperature range of 1050 to 1300 ° C.
  • the reheating temperature is less than a certain range, the problem of excessive rolling load during hot rolling may occur, or a problem that the alloy component is not sufficiently dissolved may occur, so that the present invention can limit the lower limit of the slab reheating temperature range to 1050 ° C. have.
  • the reheating temperature exceeds a certain range, the grains may grow excessively and the strength may decrease, or the re-heating may exceed the solidus temperature of the steel material, thereby deteriorating the hot rolling property of the steel material.
  • the upper limit of the range can be limited to 1300 ° C.
  • the hot rolling process includes a rough rolling process and a finish rolling process, and the reheated slab may be hot rolled and provided as a hot rolled material.
  • the hot finish rolling is preferably carried out in a temperature range of 800 ⁇ 1050 °C. If the hot finish rolling temperature is less than a certain range, excessive rolling load due to an increase in the rolling load may be a problem, and if the hot finish rolling temperature exceeds a certain range, the grains grow coarsely and the target strength cannot be obtained.
  • the hot rolled hot rolled material may be cooled to a cooling stop temperature of 600 ° C. or less at a cooling rate of 1 to 100 ° C./s. If the cooling rate is less than a certain range, the ductility of the steel may be reduced due to carbides precipitated at the grain boundary during cooling, and thus deterioration of abrasion resistance may be a problem. Therefore, the present invention can limit the cooling rate of the hot rolled material to 1 ° C / s or more. have. The lower limit of the more preferable cooling rate may be 10 ° C / s, and accelerated cooling may be applied.
  • the present invention sets the upper limit of the cooling rate to 100 ° C. Can be limited to / s.
  • the present invention limits the cooling stop temperature to 600 ° C. or less. You can.
  • the high-manganese steel with excellent oxygen-cutting properties prepared as described above contains 95% by area or more of austenite as a microstructure, has a permeability of 1.02 or less, a yield strength of 240MPa or more, a tensile strength of 720MPa or more, and an elongation of 25% or more, At the same time as having an excellent cutting surface during oxygen cutting, it is possible to effectively prevent a decrease in productivity of the oxygen cutting operation.
  • the slab that satisfies the alloy composition of Table 1 below was reheated at a temperature of 1200 ° C, hot rolled under the conditions of Table 2 to produce a hot rolled material having a thickness of 12mm, and then cooled to a cooling stop temperature of 100 ° C at a cooling rate of 20 ° C / s.
  • the specimen was prepared by accelerated cooling.
  • the yield strength, tensile strength and elongation of each specimen were measured, and the permeability, the maximum cutting speed, and the cutting surface state are shown together in Table 2 below.
  • the maximum cutting speed means the maximum cutting speed applicable when oxygen cutting is performed at an average gas pressure of 0.7 MPa.
  • the cut surface scores were evaluated by dividing them into 1, 1.5, and 2.
  • a rating of 1 means that the base material is not only melted during oxygen cutting, but also means that the average surface roughness of the cut surface is greater than 0.5 mm.
  • a rating of 1.5 means that some of the base material is melted during oxygen cutting, but the average surface roughness of the cut surface is 0.5 mm. The following means the case, and a rating of 1 means that the base material is not melted during oxygen cutting and the average surface roughness of the cut surface is 0.5 mm or less.
  • the cutability index in Table 2 means the value obtained by multiplying the maximum cutting speed of each specimen and the cutting surface rating.
  • Example 1 0.41 21.7 0.27 0.017 0.003 0.013 2.01 0.013 772.6
  • Example 2 0.18 22.3 0.14 0.019 0.010 1.80 0.00 0.013 1197.6
  • Example 3 0.44 24.6 0.26 0.019 0.007 0.020 3.45 0.018 495.4
  • Example 4 0.18 21.8 0.21 0.016 0.003 0.026 2.00 0.016 924.3
  • Example 5 0.41 21.8 0.22 0.019 0.003 0.016 1.95 0.013 779.0
  • Example 6 0.40 21.6 0.20 0.018 0.003 0.025 0.00 0.014 1062.5
  • Example 7 0.41 21.9 0.21 0.019 0.003 0.027 4.00 0.016 490.1
  • Example 8 0.39 22.3 0.15 0.018 0.009 1.93 1.92 0.016 789.9
  • Example 9 0.2 22 0.2 0.018 0.002 0.025 0 0.015 1187.2
  • Example 10 0.2 20 0.2
  • FIG. 1 (a) is a photograph of whether a spark is generated during oxygen cutting in Example 2 and a cut surface due to oxygen cutting
  • FIG. 1 (b) shows whether spark is generated during oxygen cutting in Comparative Example 2 and when oxygen is cut. This is a photograph of the cut surface.
  • FIG. 1 (b) of FIG. 1 in the case of Example 2, while having an excellent cutting surface, in the case of Comparative Example 2, excessive sparking occurs when oxygen is cut, resulting in melting of the base material, and thus not uniform It can be seen that an unsuccessful cut surface is realized.

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Abstract

L'invention porte sur de l'acier à haute teneur en manganèse ayant d'excellentes propriétés de coupe à l'oxygène qui comprend 0,1 à 0,5 % en poids de carbone (C), 20 à 26 % en poids de manganèse (Mn), 0,05 à 0,4 % en poids de silicium (Si), au plus 2,0 % en poids d'aluminium (Al) et au plus 4 % en poids de chrome (Cr), le reste étant du Fe et d'autres impuretés inévitables et qui a une sensibilité de coupe (Sc), calculée selon l'[expression relationnelle 1] ci-dessous, d'au moins 430 et peut comprendre au moins 95 % en surface d'austénite en tant que microstructure. [Expression relationnelle 1] sensibilité de coupe (Sc) = 1742 - 662 x [C]- 19,2 x [Mn] + 1,6 x [Al]-140 x [Cr] (dans l'[expression relationnelle 1], [C], [Mn], [Al], et [Cr] représentent les pourcentages respectifs en poids de C, Mn, Al, et Cr inclus dans l'acier et, si les éléments concernés ne sont pas inclus, représentent 0.)
PCT/KR2019/014184 2018-10-25 2019-10-25 Acier à haute teneur en manganèse ayant d'excellentes propriétés de coupe à l'oxygène et procédé de fabrication s'y rapportant WO2020085855A1 (fr)

Priority Applications (2)

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CN201980069176.3A CN112912526B (zh) 2018-10-25 2019-10-25 氧气切割性优异的高锰钢材及其制备方法
EP19876472.2A EP3872214A4 (fr) 2018-10-25 2019-10-25 Acier à haute teneur en manganèse ayant d'excellentes propriétés de coupe à l'oxygène et procédé de fabrication s'y rapportant

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KR10-2018-0128502 2018-10-25
KR20180128502 2018-10-25
KR1020190118923A KR102245226B1 (ko) 2018-10-25 2019-09-26 산소 절단성이 우수한 고망간 강재 및 그 제조방법
KR10-2019-0118923 2019-09-26

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WO2020085855A1 true WO2020085855A1 (fr) 2020-04-30

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Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1993013233A1 (fr) * 1991-12-30 1993-07-08 Pohang Iron & Steel Co., Ltd. Acier austenitique au manganese presentant une plasticite, une resistance et une soudabilite ameliorees, et son procede de fabrication
KR20060040718A (ko) * 2003-07-22 2006-05-10 위시노 높은 강도와 우수한 인성을 갖는 냉간 성형에 적합한오스테나이트 철강/탄소강/망간 강판의 제조 방법 및 그에따라 제조된 강판
KR20090043508A (ko) * 2006-07-11 2009-05-06 아르셀러미탈 프랑스 지연 균열에 대해 우수한 내성을 갖는 철-탄소-망간 오스테나이트계 강 시트의 제조 공정, 및 이에 의해 제조되는 시트
KR20100064473A (ko) 2008-12-05 2010-06-15 (주) 아이엔티 산소절단 장치
JP2013023742A (ja) * 2011-07-22 2013-02-04 Kobe Steel Ltd 非磁性鋼線材又は棒鋼
KR20170075657A (ko) * 2015-12-23 2017-07-03 주식회사 포스코 열간 가공성이 우수한 비자성 강재 및 그 제조방법

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1993013233A1 (fr) * 1991-12-30 1993-07-08 Pohang Iron & Steel Co., Ltd. Acier austenitique au manganese presentant une plasticite, une resistance et une soudabilite ameliorees, et son procede de fabrication
KR20060040718A (ko) * 2003-07-22 2006-05-10 위시노 높은 강도와 우수한 인성을 갖는 냉간 성형에 적합한오스테나이트 철강/탄소강/망간 강판의 제조 방법 및 그에따라 제조된 강판
KR20090043508A (ko) * 2006-07-11 2009-05-06 아르셀러미탈 프랑스 지연 균열에 대해 우수한 내성을 갖는 철-탄소-망간 오스테나이트계 강 시트의 제조 공정, 및 이에 의해 제조되는 시트
KR20100064473A (ko) 2008-12-05 2010-06-15 (주) 아이엔티 산소절단 장치
JP2013023742A (ja) * 2011-07-22 2013-02-04 Kobe Steel Ltd 非磁性鋼線材又は棒鋼
KR20170075657A (ko) * 2015-12-23 2017-07-03 주식회사 포스코 열간 가공성이 우수한 비자성 강재 및 그 제조방법

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