US20120288396A1 - Austenite steel material having superior ductility - Google Patents

Austenite steel material having superior ductility Download PDF

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Publication number
US20120288396A1
US20120288396A1 US13/519,343 US201013519343A US2012288396A1 US 20120288396 A1 US20120288396 A1 US 20120288396A1 US 201013519343 A US201013519343 A US 201013519343A US 2012288396 A1 US2012288396 A1 US 2012288396A1
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United States
Prior art keywords
steel
austenite
inventive
manganese
carbon
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Abandoned
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US13/519,343
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English (en)
Inventor
Soon-Gi Lee
Jong-Kyo Choi
Hyun-Kwan Cho
Hee-Goon Noh
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Posco Holdings Inc
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Posco Co Ltd
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Publication date
Priority claimed from KR1020090132105A external-priority patent/KR101322170B1/ko
Priority claimed from KR1020100133641A external-priority patent/KR101253860B1/ko
Application filed by Posco Co Ltd filed Critical Posco Co Ltd
Assigned to POSCO reassignment POSCO ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: CHO, HYUN-KWAN, CHOI, JONG-KYO, LEE, SOON-GI, NOH, HEE-GOON
Publication of US20120288396A1 publication Critical patent/US20120288396A1/en
Abandoned legal-status Critical Current

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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
    • C22C38/04—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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/20—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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese

Definitions

  • the present invention relates to austenite steels having excellent wear resistance, corrosion resistance, or non-magnetic performance as well as ductility, as steels used for industrial machines and in structures requiring ductility and wear resistance, superconducting application devices and general electric devices requiring non-magnetic properties, in the mining, transportation, and storage sectors as well as in oil and gas industries such as steel for a expansion pipe, steel for a slurry pipe, or sour resistant steel.
  • non-magnetic steels for use as structural materials in superconducting application devices, such as a linear motor car track and a fusion reactor, and general electric devices
  • a typical example of non-magnetic steel is AISI 304 (18Cr-8Ni base) austenitic stainless steel.
  • AISI 304 austenitic stainless steel may be uneconomical because the yield strength thereof is low and large amounts of expensive elements, such as Cr and Ni, are included therein.
  • austenitic steels may exhibit magnetic properties due to a ferromagnetic ferrite phase induced by deformation-induced transformation and thus, there may be limitations in the uses and applications thereof.
  • High-manganese austenitic steels have been continuously developed, in which expensive nickel in the austenitic stainless steels is replaced by manganese. With respect to the high-manganese austenitic steels, it is essential to secure stability of an austenite structure through appropriate changes in contents of manganese and carbon. In the case that the content of manganese is high, a stable austenite structure may be obtained even with a low content of carbon. However, in the case that the content of manganese is low, a large amount of carbon must be added for austenitization. As a result, carbides are precipitated by forming a network along austenite grain boundaries at high temperatures and the precipitates may rapidly decrease physical properties of the steel, in particular, ductility.
  • An aspect of the present invention provides an alloy having improved ductility and wear resistance by stabilizing austenite through appropriate control of contents of carbon and manganese and economically inhibiting generation of carbides in a network form that may be formed at austenite grain boundaries.
  • an austenite steel having excellent ductility including: 8 wt % to 15 wt % of manganese (Mn); 3 wt % or less (excluding 0 wt %) of copper (Cu); a content of carbon (C) satisfying relationships of 33.5C+Mn ⁇ 25 and 33.5C ⁇ Mn ⁇ 23; and iron (Fe) as well as unavoidable impurities as a remainder.
  • the steel may further include 8 wt % or less (excluding 0 wt %) of chromium (Cr).
  • the steel may further include 0.05 wt % or less (excluding 0 wt %) of titanium (Ti) and 0.1 wt % or less (excluding 0 wt %) of niobium (Nb).
  • Yield strength of the steel may be 500 MPa or more.
  • the steel may further include 0.002 wt % to 0.2 wt % of nitrogen (N).
  • a microstructure of the steel may include austenite having an area fraction of 95% or more.
  • Magnetic permeability of the steel may be 1.01 or less at a tensile strain of 20%.
  • austenite is stabilized and generation of carbides in a network form at austenite grain boundaries is inhibited by adding copper (Cu) favorable to inhibition of carbide formation with respect to manganese and appropriately controlling contents of carbon and manganese, and thus, ductility and wear resistance may be improved and corrosion resistance of steel may also be improved through the addition of chromium (Cr).
  • Cu copper
  • Cr chromium
  • FIG. 1 is a graph showing composition ranges of carbon and manganese of the present invention
  • FIG. 2 is a photograph showing an example of a microstructure of a steel sheet according to the present invention.
  • FIG. 3 is a photograph showing another example of a microstructure of a steel sheet according to the present invention.
  • the present invention may provide an austenite steel having excellent ductility by stabilizing austenite and inhibiting generation of carbides in a network form at austenite grain boundaries through controlling contents of carbon, manganese, and copper in a component system.
  • a steel having excellent ductility including 8 wt % to 15 wt % of manganese (Mn), 3 wt % or less (excluding 0 wt %) of copper (Cu), a content of carbon (C) satisfying relationships of 33.5C+Mn ⁇ 25 and 33.5C ⁇ Mn ⁇ 23, and iron (Fe) as well as unavoidable impurities as a remainder.
  • Mn as the most important element added to a high-manganese steel as in the present invention, is an element acting to stabilize austenite.
  • Mn may be included in an amount of 8% or more so as to stabilize austenite. That is, in the case that a content of Mn is 8 wt % or less, an austenite structure may not be sufficiently obtained because ferrite, a ferromagnetic phase, becomes a main structure. Also, in the case that the content of Mn is greater than 15 wt %, a stable austenite structure may not be maintained because unstable ⁇ -martensite is formed and easily transformed into ferrite according to deformation. As a result, magnetic properties may increase and fatigue properties may deteriorate, and also, a decrease in corrosion resistance, difficulty in a manufacturing process, and increases in manufacturing costs may be obtained due to the excessive addition of manganese.
  • C is an element that allows an austenite structure to be obtained at room temperature by stabilizing austenite and has an effect of increasing strength and wear resistance of steel.
  • carbon functions to decrease Ms or Md, a transformation point from austenite to martensite by a cooling process or working.
  • a content of C in the present invention may simultaneously satisfy relationships of 33.5C+Mn ⁇ 25 and 33.5C ⁇ Mn ⁇ 23 and content ranges of carbon and manganese controlled in the present invention may be confirmed in FIG. 1 .
  • a value of 33.5C+Mn is less than 25, an alpha-martensite structure, a ferromagnetic phase, may be formed because stabilization of austenite is insufficient, and thus, a sufficient amount of an austenite structure may not be obtained.
  • a value of 33.5C ⁇ Mn is greater than 23
  • carbides are excessively formed at grain boundaries because the content of C becomes excessively high, and thus, physical properties of a material may rapidly deteriorate. Therefore, the contents of carbon and manganese are required to be controlled in the foregoing ranges and as a result, sufficient austenite may be secured and the inhibition of carbide formation may be possible. Therefore, ductility and non-magnetic properties may be improved.
  • Cu has very low solubility in carbide and low diffusivity in austenite, and thus, is concentrated at an interface between the austenite and the nucleated carbide. As a result, Cu effectively delays growth of the carbide by inhibiting diffusion of carbon and eventually, has an effect of inhibiting carbide formation.
  • hot workability of steel may be decreased in the case that a content of Cu is greater than 3 wt %, an upper limit thereof may be limited to 3 wt %.
  • Cu may be added to an amount of 0.3 wt % or more, and for example, it is more effective to maximize the foregoing effect in the case that Cu is added in an amount of 2 wt % or more.
  • corrosion resistance of the steel may be additionally improved by further including 8 wt % or less (excluding 0 wt %) of chromium (Cr).
  • manganese is an element decreasing corrosion resistance of steel and corrosion resistance of the steel having the foregoing range of Mn may be lower than that of a general carbon steel.
  • corrosion resistance may be improved by the addition of Cr.
  • ductility may be increased by stabilizing austenite through the addition of Cr having the foregoing range and strength may also be increased by solution strengthening.
  • a content of Cr is greater than 8 wt %
  • manufacturing costs may not only increase, but also, resistance to sulfide stress corrosion cracking may be decreased by forming carbides along grain boundaries as well as carbon dissolved in a material and a sufficient fraction of austenite may not be obtained due to formation of ferrites. Therefore, an upper limit thereof may be limited to 8 wt %.
  • Cr may be added in an amount of 2 wt % or more. Corrosion resistance is improved by the addition of Cr and thus, the steel of the present invention may be widely used in a steel for a slurry pipe or sour resistance steel.
  • yield strength of the steel may be further improved by including 0.05 wt % or less (excluding 0 wt %) of titanium (Ti) and 0.1 wt % or less (excluding 0 wt %) of niobium (Nb) and thus, the steel having a yield strength of 500 MPa or more may be obtained.
  • Ti combines with nitrogen to form TiN and thus, exhibits an effect of increasing yield strength of steel by inhibiting growth of austenite grains at high temperatures.
  • an upper limit thereof may be limited to 0.05 wt %.
  • Nb is an element increasing strength through dissolution and precipitation hardening effects, and in particular, may improve yield strength through grain refinement during low-temperature rolling by increasing a recrystallization stop temperature (Tnr) of steel.
  • Tnr recrystallization stop temperature
  • Nb is added in an amount of greater than 0.1 wt %, physical properties of the steel may be rather deteriorated due to formation of coarse precipitates. Therefore, an upper limit thereof may be limited to 0.1 wt %.
  • the effect of the present invention may be further improved.
  • Nitrogen is an element stabilizing austenite with carbon and also, may improve strength of steel through solution strengthening.
  • N greatly deteriorates physical properties and non-magnetic properties by inducing deformation induced transformation into ⁇ -martensite and ⁇ -martensite according to deformation. Therefore, physical properties and non-magnetic properties of the steel may be improved by stabilizing austenite through appropriate addition of nitrogen.
  • a content of N is less than 0.002 wt %, the effect of stabilization may not be anticipated, and in the case that the content of N is greater than 0.2 wt %, physical properties of the steel may be deteriorated due to formation of coarse nitrides.
  • the content of N may be limited to a range of 0.002 wt % to 0.2 wt %.
  • N may be added to an amount of 0.05 wt % or more, non-magnetic properties may be more effectively improved through the stabilization of austenite.
  • iron (Fe) and other unavoidable impurities are included as a remainder.
  • unintended impurities may be inevitably incorporated from raw materials or a surrounding environment during a typical steelmaking process, the unintended impurities may not be excluded. Since the unintended impurities are obvious to those skilled in the art, detailed descriptions thereof are not particularly provided in the present specification.
  • Austenite is a main phase in the steel of the present invention having the foregoing composition and austenite may be included in an area fraction of 95% or more.
  • a targeted fraction of an austenite structure may be obtained without performing rapid cooling (water cooling) in order to inhibit grain boundary carbide precipitation, a limitation in a typical steel. That is, a targeted microstructure may be formed in the steel almost without dependency on a cooling rate and as a result, high ductility and wear resistance may be obtained. Also, corrosion resistance may be improved through the addition of Cr having the foregoing range and strength may be improved through solution strengthening.
  • the steel may have a magnetic pearmeability of 1.01 or less at a tensile strain of 20%.
  • non-magnetic properties are improved by stably securing austenite, and in particular, excellent non-magnetic properties may be obtained by allowing very low magnetic permeability to be obtained even at a tensile strain of 20% through the addition of nitrogen.
  • non-magnetic properties may be further improved by controlling magnetic permeability to have a value of 1.005 or less at a tensile strain of 20%.
  • a slab satisfying the foregoing component system may be manufactured according to a typical method of manufacturing steel, and for example, the slab of the present invention may be manufactured by rough rolling and finishing rolling after reheating the slab and then cooling.
  • Inventive Examples 1 to 13 were steels satisfying the component systems and composition ranges controlled in the present invention and it may be understood that deterioration of physical properties due to grain boundary carbide formation were not obtained even by slow cooling. Specifically, since area fractions of austenite were 95% or more and magnetic permeabilities were stably maintained even at a tensile strain of 20%, non-magnetic properties as well as elongations and yield strengths were excellent. Also, since weight losses of the samples were low, wear resistance may be secured.
  • Inventive Examples 5 to 13 it may be understood that corrosion resistances were also improved because corrosion rates were slow in the corrosion evaluation tests according to additional addition of Cr. That is, it may be confirmed that Inventive Examples 5 to 13 had effects of improving corrosion resistance better than those of Inventive Examples 1 to 4 in which Cr was not added. Further, it may be understood that Inventive Example 10 had a better effect of improving corrosion resistance, because Cu was added to an amount of 2 wt % or more, a more desirable amount. Also, in Inventive Examples 4 and 11 to 13, yield strengths were improved by further additions of Ti and Nb, and thus, were 500 MPa or more.
  • Comparative Example 1 had a value of 33.5C+Mn of 23, which did not correspond to the range controlled in the present invention.
  • a content of carbon as an austenite-stabilizing element was insufficient and as a result, targeted austenite structure and elongation were not obtained due to formation of a large amount of martensites.
  • Comparative Example 3 had a value of 33.5C+Mn of 24, which did not correspond to the range controlled in the present invention.
  • ⁇ -martensite a semi-stable phase
  • an austenite structure having a targeted area fraction may not be obtained.
  • the semi-stable ⁇ -martensite phase was easily transformed into deformation-induced martensite during subsequent deformation, very high magnetic permeability may be obtained at a tensile strain of 20%. Thus, it may be confirmed that non-magnetic properties were poor.
  • Comparative Example 4 had a value of 33.5C ⁇ Mn of 30, which did not correspond to the range controlled in the present invention.
  • austenite was formed in an amount of less than 95%. Thus, a targeted microstructure may not be obtained and as a result, elongation was very low.
  • Comparative Example 9 had a composition of AISI 1045 steel, a general carbon steel for machine structural use. Since a content of Mn was very low and Cu was not added, a weight loss of the sample according to the wear test was 0.75 g, and it may be confirmed that a wear amount was relatively larger than those of Inventive Examples.
  • Comparative Example 10 had a composition of API X70 grade steel. Likewise, since a content of Mn was very low and Cu was not added, a weight loss of the sample was greater than 1 g, and it may be confirmed that wear resistance was very poor.
  • Comparative Example 11 had a composition of API K55 grade steel. Likewise, since a content of Mn was very low and Cu was not added, a weight loss of the sample was 0.9 g, and it may be confirmed that wear resistance was very poor.
  • Comparative Example 12 was a high-manganese austenitic Hadfield steel widely used as a wear resistant steel. Since contents of C and Mn were sufficient, weight loss according to the wear test was 0.59 g, and thus, excellent wear resistance properties were obtained. However, since the inhibition of carbide formation was not facilitated due to no addition of Cu and water cooling must be performed after a long austenitization treatment at a high temperature in order to inhibit the carbide formation, there may be a limitation in a thickness of applied steel and there may have many constraints in manufacturing steel such as difficulty in using in a weld structure. Also, since Cr was not added, corrosion resistance targeted in the present invention may not be secured.
  • FIG. 2 is a micrograph of a steel sheet manufactured according to Inventive Example 1
  • FIG. 3 is a micrograph of a steel sheet manufactured according to Inventive Example 5. Since almost all structures were austenitic, it may be confirmed that stabilization of austenite may be effectively achieved by control of the component system and the composition range of the present invention.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Manufacture And Refinement Of Metals (AREA)
US13/519,343 2009-12-28 2010-12-28 Austenite steel material having superior ductility Abandoned US20120288396A1 (en)

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
KR1020090132105A KR101322170B1 (ko) 2009-12-28 2009-12-28 연성이 우수한 강재
KR10-2009-0132105 2009-12-28
KR1020100133641A KR101253860B1 (ko) 2010-12-23 2010-12-23 내식성 및 내마모성이 우수한 고연성 강재
KR10-2010-0133641 2010-12-23
PCT/KR2010/009393 WO2011081393A2 (ko) 2009-12-28 2010-12-28 연성이 우수한 오스테나이트 강재

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US (1) US20120288396A1 (de)
EP (1) EP2520684B9 (de)
JP (1) JP5668081B2 (de)
CN (1) CN102906294A (de)
CA (1) CA2785318C (de)
WO (1) WO2011081393A2 (de)

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US20150115749A1 (en) * 2013-10-31 2015-04-30 General Electric Company Dual phase magnetic material component and method of forming
US20160203899A1 (en) * 2013-10-31 2016-07-14 General Electric Company Graded magnetic component and method of forming
US20160203898A1 (en) * 2013-10-31 2016-07-14 General Electric Company Multi-phase magnetic component and method of forming
US9650703B2 (en) 2011-12-28 2017-05-16 Posco Wear resistant austenitic steel having superior machinability and toughness in weld heat affected zones thereof and method for producing same
US10655196B2 (en) 2011-12-27 2020-05-19 Posco Austenitic steel having excellent machinability and ultra-low temperature toughness in weld heat-affected zone, and method of manufacturing the same
EP3730649A4 (de) * 2017-12-22 2020-10-28 Posco Stahlmaterial mit ausgezeichneter verschleissfestigkeit und herstellungsverfahren dafür
US11661646B2 (en) 2021-04-21 2023-05-30 General Electric Comapny Dual phase magnetic material component and method of its formation
US11926880B2 (en) 2021-04-21 2024-03-12 General Electric Company Fabrication method for a component having magnetic and non-magnetic dual phases

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US20140356220A1 (en) * 2011-12-28 2014-12-04 Posco Wear resistant austenitic steel having superior machinability and ductility, and method for producing same
US10041156B2 (en) 2012-12-26 2018-08-07 Posco High strength austenitic-based steel with remarkable toughness of welding heat-affected zone and preparation method therefor
KR101490567B1 (ko) * 2012-12-27 2015-02-05 주식회사 포스코 용접성이 우수한 고망간 내마모강 및 그 제조방법
KR101611697B1 (ko) * 2014-06-17 2016-04-14 주식회사 포스코 확관성과 컬렙스 저항성이 우수한 고강도 확관용 강재 및 확관된 강관과 이들의 제조방법
KR101917473B1 (ko) * 2016-12-23 2018-11-09 주식회사 포스코 내마모성과 인성이 우수한 오스테나이트계 강재 및 그 제조방법
CN109023042A (zh) * 2018-07-25 2018-12-18 包头钢铁（集团）有限责任公司 500MPa级抗震耐氯离子腐蚀钢筋及其制造方法

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Cited By (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US10655196B2 (en) 2011-12-27 2020-05-19 Posco Austenitic steel having excellent machinability and ultra-low temperature toughness in weld heat-affected zone, and method of manufacturing the same
US9650703B2 (en) 2011-12-28 2017-05-16 Posco Wear resistant austenitic steel having superior machinability and toughness in weld heat affected zones thereof and method for producing same
US9634549B2 (en) * 2013-10-31 2017-04-25 General Electric Company Dual phase magnetic material component and method of forming
US20150115749A1 (en) * 2013-10-31 2015-04-30 General Electric Company Dual phase magnetic material component and method of forming
US20160203898A1 (en) * 2013-10-31 2016-07-14 General Electric Company Multi-phase magnetic component and method of forming
US20170183764A1 (en) * 2013-10-31 2017-06-29 General Electric Company Dual phase magnetic material component and method of forming
US10190206B2 (en) * 2013-10-31 2019-01-29 General Electric Company Dual phase magnetic material component and method of forming
US10229776B2 (en) * 2013-10-31 2019-03-12 General Electric Company Multi-phase magnetic component and method of forming
US10229777B2 (en) * 2013-10-31 2019-03-12 General Electric Company Graded magnetic component and method of forming
US20160203899A1 (en) * 2013-10-31 2016-07-14 General Electric Company Graded magnetic component and method of forming
EP3730649A4 (de) * 2017-12-22 2020-10-28 Posco Stahlmaterial mit ausgezeichneter verschleissfestigkeit und herstellungsverfahren dafür
US11661646B2 (en) 2021-04-21 2023-05-30 General Electric Comapny Dual phase magnetic material component and method of its formation
US11926880B2 (en) 2021-04-21 2024-03-12 General Electric Company Fabrication method for a component having magnetic and non-magnetic dual phases
US11976367B2 (en) 2021-04-21 2024-05-07 General Electric Company Dual phase magnetic material component and method of its formation

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EP2520684A4 (de) 2015-01-14
EP2520684A2 (de) 2012-11-07
JP2013515864A (ja) 2013-05-09
WO2011081393A3 (ko) 2011-11-10
CA2785318A1 (en) 2011-07-07
EP2520684B9 (de) 2017-01-04
CN102906294A (zh) 2013-01-30
EP2520684B1 (de) 2016-10-26
WO2011081393A2 (ko) 2011-07-07
JP5668081B2 (ja) 2015-02-12
CA2785318C (en) 2014-06-10

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