EP3730649A1 - Stahlmaterial mit ausgezeichneter verschleissfestigkeit und herstellungsverfahren dafür - Google Patents

Stahlmaterial mit ausgezeichneter verschleissfestigkeit und herstellungsverfahren dafür Download PDF

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EP3730649A1
EP3730649A1 EP18890993.1A EP18890993A EP3730649A1 EP 3730649 A1 EP3730649 A1 EP 3730649A1 EP 18890993 A EP18890993 A EP 18890993A EP 3730649 A1 EP3730649 A1 EP 3730649A1
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steel
component
excluding
relational expression
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English (en)
French (fr)
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EP3730649A4 (de
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Yong-Jin Kim
Young-Deok JUNG
Myeong-Hun KANG
Yeo-Sun YUN
Soo-Gil Park
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Posco Holdings Inc
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Posco 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
    • C22C38/18—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
    • 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
    • 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
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, 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
    • 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
    • C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
    • 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
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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 disclosure relates to an austenitic steel material, used for steels in the fields of mining, transportation, storage, and the like, in the oil and gas industries, as steels for industrial machinery, structural materials and slurry pipes, and as sour-resistant steel and the like, and a method of manufacturing the same, and more particularly, to an austenitic steel material having excellent internal quality and wear resistance, and a method of manufacturing the same.
  • Austenitic steels are used for a variety of applications due to their excellent work hardenability, low-temperature toughness, and non-magnetic properties.
  • carbon steel composed of ferrite or martensite as a main structure which has been mainly used, has limitations in its properties
  • the austenitic steel application has recently been increasing as a substitute for overcoming the disadvantages.
  • Hadfield steel having excellent wear resistance have been mainly used.
  • efforts to generate the austenite structure by including a high content of carbon and a large amount of manganese to increase wear resistance have been made steadily.
  • a high carbon content sharply degrades the properties of steel, especially ductility, by forming network-type carbide at high temperature along the austenite grain boundary.
  • ingots or steel slabs of high-manganese steel inevitably cause segregation by impurity elements such as P, S and the like in addition to alloying elements such as manganese and carbon during solidification.
  • impurity elements such as P, S and the like
  • alloying elements such as manganese and carbon
  • Patent Document 1 Korean Patent Application Publication No. 2016-0077558
  • An aspect of the present disclosure is to provide a steel material having excellent internal quality and wear resistance as well as excellent strength, elongation and impact toughness.
  • Another aspect of the present disclosure is to provide a method of manufacturing a steel material having excellent internal quality and wear resistance as well as excellent strength, elongation and impact toughness.
  • a steel material having excellent wear resistance includes, in weight percent, 0.55 to 1.4% of carbon (C), 12 to 23% of manganese (Mn), 5% or less (excluding 0%) of chromium (Cr), 5% or less (excluding 0%) of copper (Cu), 0.5% or less (excluding 0%) of Al, 1.0% or less (excluding 0%) of Si, 0.02% or less (including 0%) of S, 0.04% or less (including 0%) of phosphorus (P), and a balance of Fe and unavoidable impurities, wherein the steel material includes, in area%, 10% or less (including 0%) of carbide and balance austenite, as a microstructure.
  • the steel material may have a component segregation index (S) of 3.0 or less, represented by relational expression 1.
  • Component segregation index S C component in central portion of rolled material / C component in molten steel / 1.25 + Mn component in central portion of rolled material / Mn component in molten steel / 1.15 + P component in central portion of rolled material / P component in molten steel / 3.0 , where a component in the central portion indicates a component in a range of 50 ⁇ m or less in upper and lower portions of a part in which a highest component is measured in microstructure analysis at a position equal to half of a thickness of the rolled material.
  • the steel material may have a yield strength of 350 MPa or more, a uniform elongation of 20% or more, and an impact toughness of 40 J or more.
  • a method of manufacturing a steel material having excellent wear resistance includes:
  • a steel material may have excellent wear resistance, and may thus be applied to fields requiring wear resistance, across the mining, transportation, storage or industrial machinery fields in the oil and gas industries in which a relatively large amount of wear occurs.
  • the steel material may be expandably applied to fields requiring relatively high internal quality.
  • FIG. 1 is an image illustrating a defect in a central portion of a steel sheet thickness of comparative steel 4.
  • the present inventors have studied steels having superior strength and wear resistance, as compared to existing steels used in technical fields in which wear resistance is required, and have recognized that, in the case of high manganese steels, excellent strength and elongation, unique to austenitic steels, may be secured, and furthermore, excellent wear resistance may be secured as the hardness of the material may be increased due to work hardening of the material itself in an abrasive environment when improving a work hardening rate, thereby completing the present disclosure.
  • An exemplary embodiment of the present disclosure provides an austenitic steel material having excellent strength as well as superior strength and elongation characteristics unique to austenite-based steel materials, as the hardness of the material was increased due to work hardening of the material itself in an abrasive environment.
  • casting conditions and reheating conditions may be relatively optimized to provide an improved austenitic wear-resistant steel material having improved internal quality (central portion quality) and a method of manufacturing the same, by controlling the embrittlement of the core due to impurities such as P or the like, and large amounts of carbon and manganese, which are problems with existing austenitic wear-resistant steels.
  • a steel material having excellent wear resistance includes, in weight percent, 0.55 to 1.4% of carbon (C), 12 to 23% of manganese (Mn), 5% or less (excluding 0%) of chromium (Cr), 5% or less (excluding 0%) of copper (Cu), 0.5% or less (excluding 0%) of Al, 1.0% or less (excluding 0%) of Si, 0.02% or less (including 0%) of S, 0.04% or less (including 0%) of phosphorus (P), and a balance of Fe and unavoidable impurities.
  • the steel material includes 10 area% or less (including 0%) of carbide and balance austenite, as a microstructure.
  • Carbon (C) is an austenite stabilizing element, which not only serves to improve the uniform elongation, but also is a significantly advantageous element for improving strength and increasing a work hardening rate. If the carbon content is less than 0.55%, it may be difficult to form stable austenite at room temperature, and there is a problem that it may be difficult to secure sufficient strength and work hardening rate. On the other hand, if the content exceeds 1.4%, a large amount of carbide is precipitated to reduce the uniform elongation, and thus, it may be difficult to secure excellent elongation, causing wear resistance deterioration and premature fracture.
  • the content of C may be preferably limited to 0.55 to 1.4%, and in detail, limited to 0.8 to 1.3%.
  • Manganese (Mn) is a significantly important element that plays a role in stabilizing austenite and improves uniform elongation. To obtain austenite as a main structure in an exemplary embodiment of the present disclosure, it may be preferable that Mn is included in 12% or more.
  • the austenite stability may decrease, and thus, a martensite structure may be formed. Therefore, if the austenite structure is not sufficiently secured, it may be difficult to secure a sufficient uniform elongation.
  • the Mn content exceeds 23%, not only does the manufacturing cost increase, but also there are problems such as corrosion resistance deterioration due to manganese addition, difficulty in a manufacturing process, and the like.
  • the Mn content may be preferably limited to 12 to 23%, and in detail, 15 to 21%.
  • Chromium (Cr) stabilizes austenite up to a range of an appropriate addition amount, thereby improving impact toughness at low temperatures, and is solidified in austenite to increase the strength of steel.
  • chromium is also an element that improves the corrosion resistance of steel materials.
  • the content of Cr exceeds 5%, it may not be preferable because excessively formed carbides at the austenite grain boundary may significantly reduce toughness of steel. Also, in some cases, the content may be limited to 3.5% or less.
  • Copper (Cu) has a significantly low solid solubility in carbide and has slow diffusion in austenite, to be concentrated at an austenite and nucleated carbide interface, thereby hindering diffusion of carbon, such that the growth of carbide effectively slows. Therefore, eventually, there is an effect of suppressing generation of carbide.
  • the content of Cu exceeds 5%, there is a problem of deteriorating hot workability of the steel, and thus, it may be preferable to limit the upper limit of the content to 5%.
  • Aluminum (Al) and silicon (Si) are components added as a deoxidizer during the steelmaking process, and the upper limit of the aluminum (Al) content is limited to 0.5%, and the upper limit of the silicon (Si) content may be preferably limited to 1.0%..
  • S is an impurity and may be preferably suppressed as much as possible, and the upper limit thereof may be preferably managed to be 0.02%.
  • P is well known as an element that causes hot brittleness by segregation at the grain boundary.
  • high alloy steels containing a large amount of C and Mn such as in the steel according to an exemplary embodiment of the present disclosure, may cause serious brittleness for slabs and products in a case in which P segregation is added.
  • P exceeds a certain content, the segregation degree rises rapidly, and thus, it may be preferable to limit the content to 0.04% or less.
  • a steel material having excellent wear resistance according to an exemplary embodiment of the present disclosure includes, in area%, 10% or less (including 0%) of carbide and residual austenite, as a microstructure.
  • the fraction of the carbide exceeds 10% by area, rapid impact toughness deterioration may be caused.
  • the austenite improves ductility and toughness.
  • the steel material may preferably have a component segregation index (S) of 3.0 or less.
  • Component segregation index S C component in central portion of rolled material / C component in molten steel / 1.25 + Mn component in central portion of rolled material / Mn component in molten steel / 1.15 + P component in central portion of rolled material / P component in molten steel / 3.0 , (where a component in the central portion indicates a component in a range of 50 ⁇ m or less in upper and lower portions of a part in which a highest component is measured in microstructure analysis at a position equal to half of a thickness of the rolled material).
  • the probability of occurrence of cracks along the segregation zone at a position of 1/2t (t: a steel thickness) during processing, for example, during cutting, may increase rapidly.
  • the steel material may have a yield strength of 350 MPa or more, a uniform elongation of 20% or more, and an impact toughness of 40 J or more.
  • a method of manufacturing a steel material having excellent wear resistance includes:
  • a steel slab is obtained by continuously casting the molten steel formed as described above under the conditions of a molten steel temperature (T c ) satisfying the following relational expression 2 and of a casting speed (V) satisfying the following relational expression 3.
  • T c molten steel temperature
  • V casting speed
  • a K value represents a value determined by the following relational expression 4.
  • a K value represents a value determined by the following relational expression 4.
  • K ° C 1536 ⁇ 69 C + 4.2 Mn + 39 P (where [C], [Mn] and [P] each indicate a content (weight%) of an element.)
  • the casting conditions depending on the component changes, as in relational expressions 2 to 4 are derived. Therefore, internal quality (core quality) defects frequently occurring in the final steel may be suppressed.
  • an excessive segregation zone may be formed in the slab, resulting in slab brittleness, and the excessive segregation zone may remain even after reheating and rolling, leading to quality defects.
  • the slab obtained by continuous casting as above is reheated.
  • the slab reheating is performed at the reheating temperature (T R ) or lower obtained by the following relational expression 5.
  • T R 1453 ⁇ 165 C ⁇ 4.5 Mn ⁇ 414 P
  • T R indicates a reheating temperature (°C)
  • [C] and [Mn] each indicate the content (weight%) of the corresponding element
  • the conditions for limiting the reheating temperature depending on the component change as in relational expression 5 above is derived. Therefore, internal quality (core quality) defects frequently occurring in the final steel may be suppressed.
  • the slab reheating temperature exceeds the T R temperature, partial melting may occur in the segregation zone in the slab, and the resulting embrittlement of the core affects a product, causing a component segregation index of the rolled material to exceed 3.0 to cause defects in the core.
  • Hot rolled steel is obtained by hot rolling the reheated slab as described above to a finish rolling temperature of 850 to 1050°C.
  • finish rolling temperature is less than 850°C, carbides may precipitate so that uniform elongation may decrease, and microstructures may become pancakes, resulting in uneven elongation due to anisotropy of the structure. If the finish rolling temperature exceeds 1050°C, grain growth may be active, which may easily cause coarsening of the grain, resulting in a decrease in strength.
  • the hot-rolled steel is cooled to 600°C or less at 5°C/sec or more.
  • the cooling rate is less than 5°C/sec, or if the cooling stop temperature exceeds 600°C, carbides may be precipitated, resulting in a problem that the elongation decreases .
  • the rapid cooling process helps ensure high solid-solubility of C and N elements in the matrix. Therefore, the cooling may be preferably carried out to 600°C or less at 5°C/sec or more.
  • the cooling rate may be, in detail, 10°C/sec or more, and in more detail, 15°C/sec or more.
  • the upper limit of the cooling rate is not particularly limited, and may be limited in consideration of the cooling capability of the equipment.
  • the hot rolled steel may also be cooled to room temperature.
  • a steel material having excellent wear resistance for example, a steel material having a yield strength of 350 MPa or more, a uniform elongation of 20% or more, and an impact toughness of 40 J or more may be manufactured.
  • Slabs were prepared by continuously casting molten steel satisfying the components and component ranges illustrated in Table 1 under the conditions in Table 2, and then, hot-rolled steels were prepared by reheating, hot rolling and cooling the slabs under the conditions in Table 3.
  • the microstructure, component segregation index, cut-crack incidence rate (%), wear resistance (g), yield strength (MPa), and uniform elongation (%) of the hot-rolled steel prepared as described above were measured, and the results are illustrated in Table 4 below.
  • the wear resistance is evaluated by measuring the reduced weight after contacting the specimen to a rotating roll while spraying a predetermined amount of sand with a sand abrasion test according to the ASTM 65 test method.
  • Component in the central portion refers to a component in a range of 50 ⁇ m or less in upper and lower portions of a part in which a highest component is measured in microstructure analysis at a position equal to half of a thickness of the rolled material.
  • Cut - crack incidence rate length of crack in central portion / total cutting length ⁇ 100
EP18890993.1A 2017-12-22 2018-12-20 Stahlmaterial mit ausgezeichneter verschleissfestigkeit und herstellungsverfahren dafür Pending EP3730649A4 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
KR1020170178865A KR102020381B1 (ko) 2017-12-22 2017-12-22 내마모성이 우수한 강재 및 그 제조방법
PCT/KR2018/016384 WO2019125023A1 (ko) 2017-12-22 2018-12-20 내마모성이 우수한 강재 및 그 제조방법

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EP3730649A1 true EP3730649A1 (de) 2020-10-28
EP3730649A4 EP3730649A4 (de) 2020-10-28

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US (1) US20210164068A1 (de)
EP (1) EP3730649A4 (de)
KR (1) KR102020381B1 (de)
CN (1) CN111492082B (de)
WO (1) WO2019125023A1 (de)

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US20210164068A1 (en) 2021-06-03
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CN111492082B (zh) 2021-10-26
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