US20180274056A1 - Wear resistant steel material excellent in toughness and internal quality, and method for manufacturing same - Google Patents

Wear resistant steel material excellent in toughness and internal quality, and method for manufacturing same Download PDF

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Publication number
US20180274056A1
US20180274056A1 US15/781,674 US201615781674A US2018274056A1 US 20180274056 A1 US20180274056 A1 US 20180274056A1 US 201615781674 A US201615781674 A US 201615781674A US 2018274056 A1 US2018274056 A1 US 2018274056A1
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United States
Prior art keywords
steel material
steel
wear resistant
internal quality
manganese
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Abandoned
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US15/781,674
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English (en)
Inventor
Yong-jin Kim
Soon-Gi Lee
Il-Cheol YI
Sung-Kyu Kim
Sang-Deok KANG
Un-Hae LEE
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Posco Holdings Inc
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Posco Co Ltd
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Assigned to POSCO reassignment POSCO ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: KANG, SANG-DEOK, KIM, SUNG-KYU, KIM, YONG-JIN, LEE, SOON-GI, LEE, Un-Hae, YI, Il-Cheol
Publication of US20180274056A1 publication Critical patent/US20180274056A1/en
Abandoned 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
    • 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
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing 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 disclosure relates to a wear resistant steel material suitable for use in industrial machinery, structural materials, steel materials for slurry pipes, steel materials in sour service, for use in the mining, transportation and storage fields, or the like, and in the oil gas industry, requiring properties such as ductility and wear resistance. More particularly, the present disclosure relates to a wear resistant steel material excellent in terms of toughness and internal quality, and a method for manufacturing the same.
  • Hadfield steel having excellent wear resistance
  • it has been attempted to increase an austenitic structure and wear resistance by providing a high content of carbon and a large amount of manganese.
  • carbon added in a large amount, allows carbides to be generated along an austenitic grain boundary in the form of a network at high temperature.
  • material properties of a steel material in detail, ductility, may be rapidly lowered.
  • An aspect of the present disclosure may provide a wear resistant steel material excellent in terms of toughness and internal quality, necessarily containing C and Mn to secure wear resistance, while effectively suppressing deterioration of central properties of a slab and a rolled material caused by the C and Mn.
  • a wear resistant steel material having excellent toughness and internal quality includes: carbon (C): 0.6 wt % to 1.3 wt %, manganese (Mn): 14 wt % to 22 wt %, a balance of iron (Fe) and other unavoidable impurities, and has a microstructure including carbides in an area fraction of 5% or less (including 0%) and residual austenite.
  • a method for manufacturing a wear resistant steel material having excellent toughness and internal quality includes: reheating a steel slab including carbon (C): 0.6 wt % to 1.3 wt %, manganese (Mn): 14 wt % to 22 wt %, a balance of iron (Fe) and other unavoidable impurities; manufacturing a hot-rolled steel plate by finish hot rolling the steel slab, having been reheated, at 850° C. to 1050° C.; and cooling the hot-rolled steel plate at a cooling rate of 5° C./s or more to 600° C. or less, wherein the reheating is performed at a temperature (T, ° C.), represented by Relationship 2, or less.
  • C and Mn refer to the weight content of the element.
  • a wear resistant steel material in which an internal quality of a steel material, in addition to toughness and wear resistance, is excellent, without the addition of alloying elements other than C and Mn, may be provided.
  • the wear resistant steel material may be advantageously applied to a field requiring wear resistance.
  • a range of applications may be expanded, such as, a field in which toughness and internal quality are required.
  • FIG. 1 is a microstructure image of Comparative Steel 4 according to an exemplary embodiment of the present disclosure, and a left image illustrates a result in which a defective portion is confirmed using a scanning electron microscope (SEM) in a UT defect test while a right image illustrates a result of EPMA measurement.
  • SEM scanning electron microscope
  • the present inventors have intensively researched a method for manufacturing a steel material having excellent internal qualities (material properties, and the like), in addition to wear resistance of a steel material.
  • an austenitic steel material which has a face-centered cubic (fcc) structure, and which is high manganese steel with high contents of carbon and manganese, is used, manufacturing conditions, for controlling a steel central embrittlement problem caused by containing a large amount of carbon and manganese, are optimized.
  • fcc face-centered cubic
  • an austenitic steel material has been used for various purposes due to the properties of steel itself such as work hardenability, non-magnetic properties, and the like.
  • carbon steel mainly composed of ferrite or martensite which has been mainly used, has limitations on the required material properties
  • an application of the austenitic steel material is increasing as a substitute for overcoming shortcomings of the carbon steel mainly composed of ferrite or martensite.
  • an alloy composition preferably includes carbon (C): 0.6 wt % to 1.3 wt % and manganese (Mn): 14 wt % to 22 wt %.
  • the content of each component means weight % unless otherwise specified.
  • Carbon (C) an austenite stabilizing element, serves not only to improve a uniform elongation but also to enhance the strength and increase the strain hardening rate. If the content of carbon is less than 0.6%, it is difficult to form stable austenite at room temperature and it is difficult to secure sufficient strength and strain hardening rate. On the other hand, if the content carbon exceeds 1.3%, a large amount of carbides is precipitated, so the uniform elongation is reduced. Thus, it may be difficult to secure an excellent elongation, and it is not preferable because there are problems of a reduction in wear resistance and early fracture initiation.
  • the content of C is preferably limited to 0.6 to 1.3%.
  • Manganese (Mn) is an important element for stabilizing austenite and has an effect of improving the uniform elongation.
  • Mn is preferably contained in an amount of 14% or more.
  • the content of Mn is preferably limited to 14% to 22%, more preferably, more than 15%.
  • the remainder of the present disclosure is iron (Fe).
  • impurities not intended, may be inevitably incorporated from a raw material or a surrounding environment, so such impurities cannot be excluded. All of these impurities are not specifically described in this specification, as they are commonly known to those skilled in the art of steelmaking.
  • the wear resistant steel material of the present disclosure satisfying an alloy composition described above preferably has an austenitic single phase, as a microstructure. However, it may contain a portion of carbides, inevitably formed in a manufacturing process, and the carbides may be preferably included in an area fraction of 5% or less (including 0%).
  • the carbides are formed to be concentrated in a grain boundary having higher energy as compared to an interior of a grain. If the carbides are included in an area fraction of more than 5%, ductility is reduced. Thus, there is a problem in that it may be difficult to secure desired levels of toughness, wear resistance, and the like, in the preset disclosure.
  • the wear resistant steel material satisfying the alloy composition and microstructure, described above, may secure excellent wear resistance and toughness without the addition of additional alloying elements, other than C and Mn.
  • a wear resistant steel material according to the present disclosure has excellent central properties, as compared to an austenitic steel material according to the related art.
  • a degree of segregation of manganese (Mn) in a central portion of a steel material, represented by Relationship 1, is 1.16 or less.
  • a central portion of a steel material refers to a region of the steel material, located above and below a 1 ⁇ 2t position in a thickness direction, by 50 ⁇ m or less.
  • t refers to a thickness (mm).
  • a degree of segregation of manganese (Mn) in a central portion is preferably 1.16 or less, and more preferably 1.10 or less.
  • a wear resistant steel material according to the present disclosure has technical effects of not only securing toughness but also significantly reducing deterioration of a central portion, even when the content of Mn is high, for example, 14% or more, further more than 15%, without the addition of an additional alloying element, except for C and Mn.
  • the wear resistant steel material according to the present disclosure could be manufactured by preparing a steel slab satisfying an alloy composition proposed by the present disclosure, and then reheating—hot rolling—cooling the steel slab.
  • an alloy composition proposed by the present disclosure reheating—hot rolling—cooling the steel slab.
  • reheating is preferably performed at a temperature (T, ° C.), represented by Relationship 2, or less.
  • T a temperature
  • a temperature is preferable to satisfy a temperature range of 1100° C. to 1300° C.
  • C and Mn refer to the weight contents of the element.
  • the reheating is performed at a temperature exceeding the temperature (T) obtained by Relationship 2, partial melting occurs in segregation in a slab, so a center brittle phenomenon may occur.
  • T temperature obtained by Relationship 2
  • a degree of segregation of manganese in a central portion exceeds 1.16, not only is impact toughness deteriorated, but a UT defect may also be caused.
  • the reheating, performed at a temperature, exceeding the temperature (T) is not preferable.
  • the steel slab, having been reheated, is hot finish rolled to manufacture a hot-rolled steel plate.
  • hot finish rolling is preferably performed in a temperature range of 850° C. to 1050° C.
  • a temperature during the hot finish rolling is less than 850° C., a large amount of carbides may be precipitated, so a reduction in a uniform elongation may be caused. Moreover, a microstructure may be pancaked, so the difference of elongation along axis caused by structural anisotropy may occur.
  • a hot finish temperature exceeds 1050° C., there may be a problem in that a crystal grain may easily become coarsening due to the active growth of the crystal grain, so strength is lowered.
  • the hot-rolled steel plate, obtained as described above, is a thick plate with a relatively high thickness, and preferably has a thickness of 10 mm to 80 mm.
  • solid solubility of carbon (C) in a matrix structure may be secured to be high.
  • cooling is preferably performed in a matrix structure at a cooling rate of 5° C./s or more to 600° C. or less.
  • cooling rate is less than 5° C./s or a cooling end temperature exceeds 600° C., there may be a problem in that C is not solidified, but is precipitated as carbides, so an elongation may be lowered.
  • the cooling is performed at a cooling rate of 10° C./s or more, and further more preferably, performed at a cooling rate of 15° C./s or more.
  • an upper limit of the cooling rate can be limited to 50° C./s in consideration of the limitation of the cooling facility.
  • a microstructure was observed using an optical microscope, and a degree of segregation of Mn in central portion is illustrated by measuring the content of Mn in a hot-rolled steel plate central portion (a region located above and below a 1 ⁇ 2t position in a thickness direction, by 50 ⁇ m or less) and the content of Mn in molten steel.
  • UT defect a ultrasonic test (UT), a non-destructive test to confirm the presence or absence of cracking inside a material using ultrasonic waves, was conducted to determine whether there is a defect (Pass or Fail).
  • impact toughness at ⁇ 40° C. was measured using a Charpy impact tester.
  • y refers to austenite
  • M refers to martensite
  • a steel material is austenitic steel, the strength, elongation, and toughness are excellent, and a degree of segregation of Mn is 1.16% or less. Thus, it is confirmed that internal quality of the steel material is excellent.
  • Comparative Steel 4 to 7 a steel alloy composition satisfies the present disclosure, but a manufacturing condition is outside of the present disclosure.
  • a reheating temperature is higher than Relationship 2
  • a degree of segregation of Mn exceeds 1.16.
  • Comparative Steel 5 to 7 correspond to the cases, in which a finish hot rolling temperature, a cooling rate, and a cooling end temperature are not satisfied with the present disclosure, respectively.
  • impact toughness was inferior.
  • FIG. 1 is a microstructure image of Comparative Steel 4, in which a degree of segregation of Mn in a central portion exceeds 1.16. In this case, as a result of EPMA measurement, it is confirmed that Mn segregation occurred. In a UT defect test, a defective portion could be confirmed.

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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)
US15/781,674 2015-12-18 2016-12-16 Wear resistant steel material excellent in toughness and internal quality, and method for manufacturing same Abandoned US20180274056A1 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
KR1020150181859A KR101714922B1 (ko) 2015-12-18 2015-12-18 인성 및 내부품질이 우수한 내마모 강재 및 그 제조방법
KR10-2015-0181859 2015-12-18
PCT/KR2016/014810 WO2017105134A1 (ko) 2015-12-18 2016-12-16 인성 및 내부품질이 우수한 내마모 강재 및 그 제조방법

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EP (1) EP3392362B1 (ja)
JP (1) JP6817303B2 (ja)
KR (1) KR101714922B1 (ja)
CN (1) CN108368585B (ja)
WO (1) WO2017105134A1 (ja)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US11427899B2 (en) * 2018-05-23 2022-08-30 Min Xia NPR steel material for rock bolt and production method thereof
EP4265773A4 (en) * 2020-12-21 2024-05-29 Posco Co Ltd HIGH MANGANESE AUSTENITIC STEEL FOR DISC BRAKES

Families Citing this family (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR102020381B1 (ko) * 2017-12-22 2019-09-10 주식회사 포스코 내마모성이 우수한 강재 및 그 제조방법
KR102488498B1 (ko) * 2019-12-19 2023-01-19 주식회사 포스코 고온 내마모성이 우수한 디스크 브레이크용 오스테나이트계 강재 및 그 제조방법
KR102488759B1 (ko) * 2019-12-19 2023-01-17 주식회사 포스코 고온강도가 우수한 디스크 브레이크용 오스테나이트계 강재 및 그 제조방법

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US2378994A (en) * 1942-07-22 1945-06-26 Electro Metallurg Co Cold rolled manganese steels
US5431753A (en) * 1991-12-30 1995-07-11 Pohang Iron & Steel Co. Ltd. Manufacturing process for austenitic high manganese steel having superior formability, strengths and weldability
US20080035248A1 (en) * 2004-11-24 2008-02-14 Philippe Cugy Method Of Producing Austenitic Iron/Carbon/Manganese Steel Sheets Having Very High Strength And Elongation Characteristics Ans Excellent Homogeneity
US20130209833A1 (en) * 2010-10-21 2013-08-15 Arcelormittal Investigacion Y Desarrollo, S.L. Hot-rolled or cold-rolled steel plate, method for manufacturing same, and use thereof in the automotive industry
US20140007992A1 (en) * 2011-01-11 2014-01-09 Thyssenkrupp Steel Europe Ag Method for Producing a Hot-Rolled Flat Steel Product

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US11427899B2 (en) * 2018-05-23 2022-08-30 Min Xia NPR steel material for rock bolt and production method thereof
EP4265773A4 (en) * 2020-12-21 2024-05-29 Posco Co Ltd HIGH MANGANESE AUSTENITIC STEEL FOR DISC BRAKES

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CN108368585B (zh) 2020-09-29
EP3392362B1 (en) 2024-05-01
JP2019504184A (ja) 2019-02-14
EP3392362A1 (en) 2018-10-24
EP3392362A4 (en) 2018-10-24
WO2017105134A1 (ko) 2017-06-22
JP6817303B2 (ja) 2021-01-20
CN108368585A (zh) 2018-08-03
KR101714922B1 (ko) 2017-03-10

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