EP2895635B1 - Stahllegierung für einen niedrig legierten, hochfesten stahl - Google Patents

Stahllegierung für einen niedrig legierten, hochfesten stahl Download PDF

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Publication number
EP2895635B1
EP2895635B1 EP13789475.4A EP13789475A EP2895635B1 EP 2895635 B1 EP2895635 B1 EP 2895635B1 EP 13789475 A EP13789475 A EP 13789475A EP 2895635 B1 EP2895635 B1 EP 2895635B1
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EP
European Patent Office
Prior art keywords
max
alloy
steel
contents
strength
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Active
Application number
EP13789475.4A
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German (de)
English (en)
French (fr)
Other versions
EP2895635A1 (de
Inventor
Philippe SCHAFFNIT
Jürgen KLABBERS-HEIMANN
Joachim Konrad
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Mannesmann Precision Tubes GmbH
Ilsenburger Grobblech GmbH
Original Assignee
Mannesmann Precision Tubes GmbH
Ilsenburger Grobblech GmbH
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Publication date
Application filed by Mannesmann Precision Tubes GmbH, Ilsenburger Grobblech GmbH filed Critical Mannesmann Precision Tubes GmbH
Priority to SI201331451T priority Critical patent/SI2895635T1/sl
Priority to PL13789475T priority patent/PL2895635T3/pl
Publication of EP2895635A1 publication Critical patent/EP2895635A1/de
Application granted granted Critical
Publication of EP2895635B1 publication Critical patent/EP2895635B1/de
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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
    • C22C38/001—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
    • C22C38/38—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
    • C22C38/18—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 method for producing a steel alloy for the production of strips, sheets and tubes for a low-alloy, high-strength carbide-free bainitic steel according to claim 1.
  • the invention relates to tubes, strips, and sheets made of this alloy, from which e.g. Components for the automotive industry, such as body panels, components of support structures or airbag tubes and cylinder tubes are produced.
  • Components for the automotive industry such as body panels, components of support structures or airbag tubes and cylinder tubes are produced.
  • wear plates made of this alloy can be used for excavator buckets.
  • steels are used for applications where sudden impact energies must be absorbed, e.g. as bulletproof armor.
  • Tubes made from this alloy can be designed as welded, hot or cold strip or seamless tubes, which may occasionally have deviating from the circular cross-sections.
  • Construction tubes or sheets of this steel alloy can also be used for highly stressed welded steel structures, for example in crane, bridge, ship, hoist and truck construction.
  • Characteristic of these steels is e.g. a strength of 1000 to about 2000 MPa, depending on the strength of an elongation at break of at least 5% and a very finely (nano-) structured bainitic structure with shares of retained austenite.
  • Carbide-free bainitic steels for rails are eg from the DE 696 31 953 T2 known.
  • the steel alloy disclosed therein in addition to additions of manganese, chromium and other elements such as molybdenum, nickel, vanadium, tungsten, titanium and boron, a silicon content between 1 and 3%.
  • This steel is designed for the requirements of highly wear-stressed rails, but for tapes, sheets and tubes for the stated application uneconomical or not applicable, since in addition to the requirements for wear resistance, both the strength and toughness requirements are met.
  • the cross-sectional dimensions of the rails differ significantly from those of the strips, sheets and tubes due to their compact cross-section, which means that the alloy concept can be adapted with regard to the required material properties after the air cooling of the steel required.
  • a disadvantage of the known steel is also the expensive addition of titanium and other alloying elements such as nickel, molybdenum and tungsten.
  • Another problem with the known steel is that no information is made on the nitrogen content, which exerts a negative influence on the material properties, in particular with aluminum additions by the formation of aluminum nitrides.
  • the object of the invention is to provide a method for producing a steel alloy for a low-alloy, high-strength, at the same time tough and wear-resistant carbide bainitic steel for the production of strips, sheets and tubes, on the one hand cheaper than the known steel alloys and on the other hand uniform, the requirements appropriate material properties, such as strength, elongation at break, toughness etc. guaranteed. moreover These material properties should be achieved by air hardening even when cooling to still air.
  • rare earths and reactive elements such as Ce, Hf, La, Re, Sc and / or Y can be alloyed with a total of up to 1 wt .-%.
  • steels according to the invention After lapping in air, steels according to the invention have a strength (R m ) of more than 1250 MPa, an elongation at break of more than 12% and a toughness (KBZ) of at least 15 J at -20 ° C. in the state of lumps or slabs (see Table 1 ) .
  • the structure consists of carbide-free bainite and retained austenite with a content of at least 75% bainitic ferrite, at least 10% retained austenite and up to a maximum of 5% martensite (or martensite phase and / or decomposed austenite).
  • the steel alloy according to the invention is based on the development of the DE 696 31 953 T2 and WO 2009/075494 A1 known carbide-free bainitic steel on.
  • chromium in the range of 0.10 to 2.00 wt .-%, moreover, the kinetics of ferrite formation can be decisively controlled, so that the formation of coarse polygonal ferrite grains, which can adversely affect the material properties, is effectively avoided.
  • Crucial here is the interaction of aluminum and chrome. While aluminum accelerates the ferritic and bainitic transformation, the addition of chromium retards ferritic transformation (see p FIG. 2 ). Through a specific combination of these two elements, both the kinetics of ferrite and bainite formation can be controlled.
  • the nitrogen content be as specified
  • the upper limit of 0.025 wt.%, Better still 0.015 wt.% Or optimally 0.010 wt ⁇ 10 -3 (wt .-%) must be satisfied.
  • a minimum content of nitrogen 0.001 wt.%, Optimally 0.0020, is required to allow niobium carbonitride formation necessary to increase the toughness by grain refining.
  • the investigated alloy compositions and the determined mechanical characteristics are given in Table 1 . All samples were heated to about 950 ° C and then cooled in still air or accelerated. The required cooling rate is made dependent on the sheet thickness and the composition. As the results of the mechanical sampling show, the required properties could not be achieved with the test melt 14 because of the too low Cr content.
  • the experimental melt 16 according to the invention fulfilled the requirements because of the larger sheet thicknesses of 12 mm only by accelerated cooling. Typical temperature profiles for cooling in still air or with quenching are in FIG. 3 shown.
  • FIG. 4 are some of the investigated experimental melts and their mechanical characteristics and cooling conditions compared to common and high strength steel materials shown. It becomes clear that the developed steel alloy encompasses the range of higher-strength materials combined with significantly improved elongation properties. The results impressively confirm the excellent mechanical properties (strength and toughness of the steel alloy according to the invention even for semi-finished products such as slabs or slabs) in the cured state ( Table 1 ).
  • TRIP Transformation Induced Plasticity
  • the stabilization of the retained austenite and the martensite start temperature are observed taking into account the cooling rate, wherein in the aforementioned.
  • empirically determined formulas the contents of C, Mn, Si, Al, Cr and Mo in wt .-% and ⁇ are used as the cooling rate in ° C / sec.
  • the units of the coefficients used in the formulas should be chosen according to the variables used in the formulas.
  • Martensite starting temperature (° C): In order to avoid larger martensitic microstructures which may degrade the mechanical and technological properties, the martensite starting temperature shall be determined as follows: 525 - 350 ⁇ C - 45 ⁇ Mn - 16 ⁇ Mo - 5 ⁇ Si + 15 ⁇ al ⁇ ⁇ 400
  • the microstructure of the steel according to the invention consists of bainitic ferrite and retained austenite lamellae. It may have fractions of up to 5% martensite (or martensite / austenite phase and / or decomposed austenite).
  • martensite or martensite / austenite phase and / or decomposed austenite.
  • the two most important parameters of the microstructure, which significantly influence the mechanical properties of the steel, are the fin spacing and the proportion of retained austenite. The smaller the fin spacing and the higher the proportion of retained austenite, the higher the strength and elongation at break of the material become.
  • the average fin spacing should be less than 750 nm, advantageously less than 500 nm.
  • a residual austenite content of at least 10% and a martensite proportion of at most 5% should be present.
  • the average former austenite grain size should not exceed a value of 100 ⁇ m.
  • the microstructure is very fine, the microstructural constituents can hardly be differentiated by light microscopy, so that a combination of electron microscopy and X-ray diffraction can be used on a case-by-case basis.
  • the result of an X-ray diffraction measurement is in FIG. 7 shown. From the intensity distribution of the X-ray spectrum, the crystal structure of the existing structural constituents and their phase components can be determined.

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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)
EP13789475.4A 2012-09-14 2013-08-28 Stahllegierung für einen niedrig legierten, hochfesten stahl Active EP2895635B1 (de)

Priority Applications (2)

Application Number Priority Date Filing Date Title
SI201331451T SI2895635T1 (sl) 2012-09-14 2013-08-28 Legirano jeklo za nizko legirano, visokotrdnostno jeklo
PL13789475T PL2895635T3 (pl) 2012-09-14 2013-08-28 Stop stalowy dla niskostopowej stali o wysokiej wytrzymałości

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102012018833 2012-09-14
PCT/DE2013/000519 WO2014040585A1 (de) 2012-09-14 2013-08-28 Stahllegierung für einen niedrig legierten, hochfesten stahl

Publications (2)

Publication Number Publication Date
EP2895635A1 EP2895635A1 (de) 2015-07-22
EP2895635B1 true EP2895635B1 (de) 2019-03-06

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US (2) US20150267282A1 (enExample)
EP (1) EP2895635B1 (enExample)
JP (1) JP6513568B2 (enExample)
KR (1) KR102079612B1 (enExample)
AR (1) AR092556A1 (enExample)
AU (2) AU2013314787A1 (enExample)
BR (1) BR112015005216A2 (enExample)
CA (1) CA2881686A1 (enExample)
CL (1) CL2015000634A1 (enExample)
DK (1) DK2895635T3 (enExample)
ES (1) ES2729562T3 (enExample)
MX (1) MX376714B (enExample)
PE (1) PE20151042A1 (enExample)
PL (1) PL2895635T3 (enExample)
RU (1) RU2620216C2 (enExample)
SI (1) SI2895635T1 (enExample)
TR (1) TR201903460T4 (enExample)
TW (1) TW201432061A (enExample)
UA (1) UA116111C2 (enExample)
WO (1) WO2014040585A1 (enExample)
ZA (1) ZA201502450B (enExample)

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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
DE102016107141A1 (de) * 2016-04-18 2017-10-19 Benteler Steel/Tube Gmbh Kraftfahrzeuganhänger, Fahrwerkachse, insbesondere für einen Kraftfahrzeuganhänger und Verwendung der Fahrwerksachse und eines Werkstoffes
CN106191666B (zh) * 2016-07-06 2018-01-02 马钢(集团)控股有限公司 一种低成本精节生产的轨道交通用贝氏体钢车轮及其制造方法
WO2018215813A1 (en) 2017-05-22 2018-11-29 Arcelormittal Method for producing a steel part and corresponding steel part
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
SE542672C2 (en) 2018-09-14 2020-06-23 Ausferritic Ab Method for producing an ausferritic steel austempered during continuous cooling followed by annealing
US12480173B2 (en) 2018-11-30 2025-11-25 Arcelormittal Cold rolled annealed steel sheet with high hole expansion ratio and manufacturing process thereof
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
US20210404028A1 (en) * 2020-01-17 2021-12-30 Indian Institute Of Technology Bombay High strength and toughness low carbon nanostructured bainitic steel and preparation method thereof
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
US20220195550A1 (en) * 2020-12-23 2022-06-23 Caterpillar Inc. Air-hardened machine components
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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Also Published As

Publication number Publication date
CL2015000634A1 (es) 2015-11-20
PE20151042A1 (es) 2015-07-27
DK2895635T3 (da) 2019-05-20
BR112015005216A2 (pt) 2022-07-26
KR20150070150A (ko) 2015-06-24
JP6513568B2 (ja) 2019-05-15
PL2895635T3 (pl) 2019-08-30
AU2018201165B2 (en) 2019-09-26
WO2014040585A1 (de) 2014-03-20
ZA201502450B (en) 2016-09-28
AU2013314787A1 (en) 2015-04-30
KR102079612B1 (ko) 2020-02-20
TR201903460T4 (tr) 2019-04-22
TW201432061A (zh) 2014-08-16
US20200131608A1 (en) 2020-04-30
JP2015533942A (ja) 2015-11-26
SI2895635T1 (sl) 2019-06-28
CA2881686A1 (en) 2014-03-20
RU2620216C2 (ru) 2017-05-23
US20150267282A1 (en) 2015-09-24
AR092556A1 (es) 2015-04-22
UA116111C2 (uk) 2018-02-12
AU2018201165A1 (en) 2018-03-22
RU2015113522A (ru) 2016-11-10
ES2729562T3 (es) 2019-11-04
MX2015003103A (es) 2015-10-22
EP2895635A1 (de) 2015-07-22
MX376714B (es) 2025-03-07

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