US20150267282A1 - Steel alloy for a low-alloy high-strength steel - Google Patents

Steel alloy for a low-alloy high-strength steel Download PDF

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Publication number
US20150267282A1
US20150267282A1 US14/428,286 US201314428286A US2015267282A1 US 20150267282 A1 US20150267282 A1 US 20150267282A1 US 201314428286 A US201314428286 A US 201314428286A US 2015267282 A1 US2015267282 A1 US 2015267282A1
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Prior art keywords
weight
steel
max
steel alloy
alloy according
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Abandoned
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US14/428,286
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English (en)
Inventor
Philippe Schaffnit
Jürgen Klabbers-Heimann
Joachim Konrad
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Ilsenburger Grobblech GmbH
Salzgitter Mannesmann Precision GmbH
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Ilsenburger Grobblech GmbH
Salzgitter Mannesmann Precision GmbH
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Assigned to ILSENBURGER GROBBLECH GMBH, SALZGITTER MANNESMANN PRECISION GMBH reassignment ILSENBURGER GROBBLECH GMBH ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: KONRAD, JOACHIM, KLABBERS-HEIMANN, Jürgen, SCHAFFNIT, Philippe
Publication of US20150267282A1 publication Critical patent/US20150267282A1/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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of 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
    • C22C38/18—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
    • 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
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C21D2211/002—Bainite

Definitions

  • the invention relates to a steel alloy for a low alloy high strength steel which at the same time is tenacious and has excellent wear resistance according to patent claim 1 .
  • the invention relates to pipes, strips and sheets made of this alloy, from which for example components for the automobile industry such as vehicle bodies, components of support structures or airbag tubes and cylinder tubes are produced.
  • wear plates made of this alloy can for example be used in case of high wear requirements for excavator shovels.
  • Such steels are also used for applications where sudden impact energies have to be absorbed, for example as bullet proof armor.
  • Pipes produced from this alloy can be configured as welded pipes that are produced from hot or cold strip or in a seamlessly, and which depending on the case can have a cross section which deviates from the circular shape.
  • Construction pipes or plates made of this alloy can also be used for welded steel constructions that are exposed to particularly high stress for example in crane construction, bridge construction, hoist construction and heavy-duty vehicle construction.
  • Characteristic for these steels is for example a strength of 1000 to about 2000 MPa, an elongation at brake of at least 5% depending on the strength and an extremely fine (nano) structured bainitic microstructure with portions of residual austenite.
  • the approach for generating this ultra-fine microstructure is based on the phase transformation at low temperatures in the bainite region while avoiding the precipitation of cementite and formation of martensite. Suppression of carbides that precipitate in the bainite such as cementite is necessary because on one hand, these have a strong embrittling effect as possible fracture inducers thereby preventing achieving the required tenacity, and on the other hand, the proportions of stabilized austenite, which are necessary for achieving the properties according to the invention, cannot be established.
  • Carbide-free bainitic steels for rail tracks are for example known from DE 696 31 953 T2. Beside manganese, chromium and further elements such as molybdenum nickel vanadium wolfram titanium and boron, the steel alloy disclosed there has a silicon content between 1 and 3%.
  • This steel is configured for the demands on rail tracks that are exposed to strong wear stress, however it cannot be used or is uneconomical for strips, sheets and pipes for the mentioned field of application because in these cases beside the demands on wear resistance, the strength and tenacity requirements also have to be met.
  • the cross sectional dimensions of rails significantly differ from those of strips, sheets and pipes which requires adjustment of the alloying concept with regard to the material properties to be achieved after air cooling of the steel.
  • a disadvantage of the known steel is also the expensive addition of titanium and other alloy elements such as nickel, molybdenum and wolfram.
  • a further problem in the known steels is that no information regarding the nitrogen content are given which adversely affects material properties in particular through formation of aluminum nitrides when aluminum is added.
  • Object of the invention is to set forth a steel alloy for a low alloy, high-strength carbide-free bainitic steel which is tenacious and wear resistant for producing strips, sheets and pipes, which on one hand is more cost effective than the known steel alloys and on the other hand ensures uniform material properties which meet the demands such as strength, elongation at break, tenacity etc. In addition, these material properties are also to be achieved when cooling at stationary air by air hardening.
  • rare earths and reactive elements such as Ce, Hf, La, Re, Sc and/or Y of a ⁇ overall up to 1 weight % can be added.
  • steels according to the invention have already after cooling at air a strength (R m ) of over 1250 MPa, an elongation at break of over 12% and a tenacity (KBZ) at ⁇ 20° C. of at least 15 J (cf. Table 1).
  • the microstructure consists of carbide-free bainite and residual austenite with a proportion of at least 75% bainitic ferrite, at least 10% residual austenite and up to maximally 5% martensite (or martensite phase and/or decomposed austenite).
  • the steel alloy according to the invention is based on the development of the carbide-free bainitic steel form DE 6906 953 T2 and WO 2009/075494 A1.
  • Tests that were carried out in the context of the present invention have surprisingly shown that compared to known steel alloys for achieving the demanded material properties already can be achieved by an air hardening by targeted addition of aluminum in the range of 0.05 to 3.0 weight % and niobium in the range of 0.001 to 0.5 weight % beside an excellent material strength and wear resistance, very good tenacity can be achieved.
  • the addition of niobium results in a significant improvement of the tenacity properties through grain refinement, so that this alloy meets the high requirements regarding mechanical properties and wear resistance.
  • the kinetic of the ferrite formation can be decisively controlled so that the formation of coarse polygonal ferrite bodies, which can adversely affect the material properties, can be effectively avoided.
  • Important in this regard is the interaction between aluminum and chromium. While aluminum accelerates the ferritic and bainitic transformation, addition of chromium delays the ferritic transformation (cf. FIG. 2 ). Targeted combination of these two elements, allows controlling the kinetic of the ferrite and bainite formation.
  • FIG. 2 The influence of different alloying elements on the kinetic of the transformation is shown in FIG. 2 .
  • the effects of C, Si, Al, Mn, Cr and Mo on the transformation kinetic of ferrite, perlite and bainite and on the martensite start temperature are shown schematically.
  • the nitrogen content does not exceed the stated upper limit of 0.025%, better 0.015% or optimally 0.010 weight % in order to minimize the number and size of the deleterious aluminum nitrides as primary precipitations in the steel, wherein in addition the condition Al ⁇ N ⁇ 5 ⁇ 10 ⁇ 3 has to be satisfied. Otherwise, a minimal content of nitrogen of 0.001 weight %, optimally 0.0020 is required in order to enable a required niobium carbonitride formation for increasing tenacity by grain refinement.
  • the tested alloy compositions and the determined mechanical characteristics are shown in Table 1. All samples where heated to about 950° C. and then cooled at stationary air or subjected to accelerated cooling. The required cooling speed is selected depending on the sheet thickness and the composition. As the results of the mechanical sampling show, the demanded properties could not be achieved with the sample melt 14 due to the too low Cr content. The test melt 16 satisfied the demands due to the greater sheet thickness of 12 mm only after accelerated cooling. Typical temperature profiles for the cooling at stationary air or with quenching are shown in FIG. 3 .
  • FIG. 4 some of the tested test melts and their mechanical characteristics and cooling conditions are shown in comparison to the conventional and high strength steel materials. It can be seen that in the developed steel the region of higher strength materials at improved stretch properties.
  • TRIP-effect With corresponding proportions of residual austenite a so called TRIP-effect can then also be advantageously used.
  • Steels which usually are referred to by the term TRIP (“Transformation Induced Plasticity”) are steels which at the same time have a very high strength and a high ductility, which makes them especially suited for cold forming. These properties are obtained owing to their special microscopic structure, wherein the deformation-induced martensite formation and the work hardening associated therewith is inhibited and the ductility is increased.
  • the effect of the TRIP effect is optimal for a residual austenite proportion of about 1 to 20%.
  • the following conditions should be adhered to for achieving the demanded material properties in particular of the mechanical technological properties for the transformation kinetic and the transformation behavior ( FIG. 2 ) the stabilizing of the residual austenite and the martensite start temperature while taking the cooling rate into account wherein in the mentioned empirically determined formulas the contents of C, Mn, Si, Al, Cr and Mo in weight % and T as cooling rate in ° C./s have to be inserted.
  • the units of the coefficients that are used in the formula are to be selected according to the variables used in the formula.
  • the martensite start temperature has to be determined as follows:
  • the microstructure of the steel according to the invention consist of ferrite and residual austenite lamellae. It can have proportions of martensite of up to 5% (or martensite/austenite phase and/or decomposed austenite).
  • the two most important characteristics of the microstructure which significantly influence the mechanical properties of the steel are the lamella spacing and the proportion of residual austenite. The smaller the lamellar interspacing and the higher the proportion of residual austenite the higher are the strength and elongation at break of the material.
  • the average lamellar interspacing should be smaller than 750 nm, advantageously smaller than 500 nm.
  • the average previous austenite grain size should not exceed a value of 100 ⁇ m.
  • the microstructure is very fine, the components of the microstructure can hardly be distinguished from each other microscopically so that depending on the case a combination of electron microscopy and x-ray diffraction has to be used.
  • the components of the microstructure can be distinguished by means of scanning electron microscopy. In this way, an average lamellar interspacing of about 300 nm was determined.
  • the result of an x-ray diffraction measurement is shown in FIG. 7 .
  • the crystal structure of the present microstructure components and their phase proportions can be determined.
  • Residual austenite proportions between 10% and 20% were determined using the x-ray diffraction method.

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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)
US14/428,286 2012-09-14 2013-08-28 Steel alloy for a low-alloy high-strength steel Abandoned US20150267282A1 (en)

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DE102012018833.1 2012-09-14
DE102012018833 2012-09-14
PCT/DE2013/000519 WO2014040585A1 (de) 2012-09-14 2013-08-28 Stahllegierung für einen niedrig legierten, hochfesten stahl

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CN105088090A (zh) 2015-08-28 2015-11-25 宝山钢铁股份有限公司 一种抗拉强度2000MPa级的防弹钢板及其制造方法
JP2018538440A (ja) 2015-11-16 2018-12-27 ベントラー スティール ／ チューブ ゲーエムベーハー 高エネルギー吸収能力を備えた合金鋼及び鋼管製品
DE102015119839A1 (de) * 2015-11-17 2017-05-18 Benteler Steel/Tube Gmbh Stahllegierung mit hohem Energieaufnahmevermögen und Stahlrohrprodukt
JP6967628B2 (ja) * 2015-12-29 2021-11-17 アルセロールミタル 超高強度合金化溶融亜鉛めっき鋼板を製造するための方法、及び得られた合金化溶融亜鉛めっき鋼板
US11035020B2 (en) * 2015-12-29 2021-06-15 Arcelormittal Galvannealed steel sheet
CN110616366B (zh) * 2018-06-20 2021-07-16 宝山钢铁股份有限公司 一种125ksi钢级抗硫油井管及其制造方法
CN109536843B (zh) * 2019-01-04 2020-08-25 武汉钢铁有限公司 一种含氮双相耐腐蚀耐磨热轧钢及生产方法
DE102019122515A1 (de) 2019-08-21 2021-02-25 Ilsenburger Grobblech Gmbh Verfahren zur Herstellung von hochfesten Blechen oder Bändern aus einem niedrig legierten, hochfesten bainitischen Stahl sowie ein Stahlband oder Stahlblech hieraus
SE543967C2 (en) * 2020-02-11 2021-10-12 Blykalla Reaktorer Stockholm Ab A martensitic steel
CN111471934B (zh) * 2020-05-25 2021-08-13 武汉钢铁有限公司 无碳化物贝氏体的自强化齿轮用钢及制备方法
CN115011867B (zh) * 2022-04-19 2023-04-14 清华大学 高强韧耐磨钢衬板及其制备方法
CN116574978B (zh) * 2023-04-23 2024-01-09 鞍钢股份有限公司 一种多阶段热处理细晶压力容器钢板及其制造方法

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AU2018201165B2 (en) 2019-09-26
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