WO2018004363A1 - Acier multiphasique, en particulier pour la fabrication de rails de voie normale - Google Patents

Acier multiphasique, en particulier pour la fabrication de rails de voie normale Download PDF

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Publication number
WO2018004363A1
WO2018004363A1 PCT/PL2016/000155 PL2016000155W WO2018004363A1 WO 2018004363 A1 WO2018004363 A1 WO 2018004363A1 PL 2016000155 W PL2016000155 W PL 2016000155W WO 2018004363 A1 WO2018004363 A1 WO 2018004363A1
Authority
WO
WIPO (PCT)
Prior art keywords
steel
phase steel
phase
rails
rail
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.)
Ceased
Application number
PCT/PL2016/000155
Other languages
English (en)
Inventor
Tomasz ZYGMUNT
Janusz KASPROWICZ
Tomasz DZIERŻAWCZYK
Stanisław WÓJCIK
Roman KUZIAK
Władysław ZALECKI
Ryszard MOLENDA
Andrzej WROŻYNA
Krzysztof RADWAŃSKI
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.)
Instytut Metalurgii Zelaza
ArcelorMittal Poland SA
Original Assignee
Instytut Metalurgii Zelaza
ArcelorMittal Poland SA
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Instytut Metalurgii Zelaza, ArcelorMittal Poland SA filed Critical Instytut Metalurgii Zelaza
Priority to US16/312,528 priority Critical patent/US20190226062A1/en
Priority to EP16907462.2A priority patent/EP3500688A4/fr
Publication of WO2018004363A1 publication Critical patent/WO2018004363A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

Links

Classifications

    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C21D9/04—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rails
    • 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
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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

Definitions

  • Multi-phase steel especially for production of standard-gauge rails
  • This invention relates to the multi-phase steel of which bainite is the most important structural component.
  • Multi-phase steel according to the invention is preferably used for production of standard-gauge rails of enhanced durability in service, specifically of enhanced resistance to contact - fatigue defects initiation and growth.
  • Composition of multi-phase steel is disclosed also in the Japanese patent application JPH02133544(A) aimed at manufacturing of high strength steel rails, characterised also by good ductility, resistance to wear, good weldability, resistance to cracking and high hardenability, obtained by using alloy additives and Ti in order to bind N to prevent against the BN formation in the steel.
  • Steel according to invention contains: 0.50 - 0.85 wt.%C, 0.10 - 1.00 wt.% Si, 0.50 - 1.50 wt.% Mn, ⁇ 0.035 wt.%P, ⁇ 0.035wt.% S, 0.05wt.% Al and 0.0005 - 0.005wt.% B, with addition of at least one constituent enhancing hardenability: 0.05 - 1.50wt.%Cr, 0.02 - 0.20wt.% Mo, 0.01 - 0.10wt.% V, 0.10 - 1.00 wt.% Ni and 0.005 - 0.50 wt.% Nb, 0.003 - 0.1 wt.% Ti, independently or in combination.
  • Rails of pearlitic and hyper-eutectoid steels show high resistance against wear, however, they are less resistant to the initiation and development of contact - fatigue defects.
  • rails of bainitic steels are characterized by superior resistance against the initiation and growth of contact - fatigue defects, however their resistance to wear is lower compared to rails of pearlitic structure subject to thermal treatment.
  • Patent subject matter is to design the multi-phase steel structure, especially for rails production, by proper design of steel chemical composition, wherein such steel after cooling down the rail in still air directly after rolling process, would exhibit high resistance to contact and fatigue defects and resistance to wear, corrugation and plastic creeping within rail head area.
  • Object of the invention is multi-phase steel, preferably used for production of standard- gauge rails, characterized by the fact that the content of basic elements in the steel is no less than:
  • multi-phase steel contains:
  • Ti in the range 0.01 - 0.25 wt.%, preferably satisfying the following relationship:
  • temperature of the bainitic transformation initiation (temperature B S ) of multi-phase steel according to the invention is no higher than 460°C, and temperature of martensitic transformation M s is no less than 300°C.
  • content of bainitic ferrite is above 70 vol. % of steel, aliotrimorphic ferrite below 10 vol.% of steel, self-tempered martensite below 10 vol. % of steel, retained austenite linked to bainitic ferrite of carbon content min. 1.25 wt.% - above 10 vol.% of steel, and the bainitic ferrite is hardened with carbon nano-particles TiC.
  • condition (1) The result of assumptions made using condition (1), equation (2), condition (3) and (4) is a unique technical solution representing an embodiment of the invention.
  • Fulfilment of the condition resulting from formula 3 prevents against cementite particles precipitation in steels resulting in the formation so called carbide-free bainite. Moreover, addition of aluminium limits segregation of alloy additives in steel during the solidification process and especially favourably affects the mechanical stability of retained austenite during contact between wheel and rail.
  • condition resulting from condition (4) for the lower limit allows for protecting boron against formation of boron nitride (BN) and at value above 0.03 wt.% leads to obtaining fine-grained austenite during the process of rails roiling and provides the capacity for bainitic ferrite strengthening with TiC nano-particles.
  • BN boron nitride
  • Nickel is used to stabilize retained austenite and to increase the resistance to cracks propagation.
  • the final content of alloy additives in steel according to invention is determined in order to get specified value of bainite start transformation temperature (Bs) and martensite transformation start temperature (Ms).
  • Bs bainite start transformation temperature
  • Ms martensite transformation start temperature
  • Temperature B s and M s is calculated using the following formulae developed by K.W. Andrews (K.W, Andrews: J. Iron and Steel Inst, 1965, 203, 721-729).
  • Standard-gauge-rails of multi-phase steel according to invention are characterized by increased resistance to contact - fatigue defects initiation in relation to pearlitic steels and comparable resistance to wear, corrugation and plastic creeping in rail's head.
  • Such combination of service properties is achieved by obtaining fine-grained austenitic structure during hot roiling process and proper phase composition of rail structure after cooling down in still air, especially by the presence of retained austenite resistant to thermal and mechanical loads.
  • Fine-grained structure of austenite is provided by the presence of fine particles of titanium nitride TiN (of dimensions less than 20 nm) in steel and dynamic precipitation of titanium carbide TiC particles during rolling.
  • Control of titanium nitride TiN particles size is realised by application of cooling conditions in a secondary cooling zone during the process of continuous casting, providing achievement of cooling rate in the ingot corner within 12-15°C/s and within the near-surface layer on the sides within 8-10°C/s,
  • Structure of multi-phase steel for production of standard-gauge rails according to the invention allows for obtaining better durability of compared to rails of pearlitic steel, cooled in still air after rolling process.
  • Designing chemical composition of multi-phase steel according to invention allows for obtaining retained austenite within the rail structure of the following parameters:
  • Retained austenite in the rail head running surface according to invention is subject initially to gradual fragmentation and transformation (TRIP effect) into martensite during contact with wheel, and then martensite is transformed into ferrite containing fine cementite particles. Prolonged - gradual transformation of austenite into martensite causes work hardening of the subsurface region during rail service, which slows down the wear processes and initiation of the contact-fatigue defects.
  • TRIP effect gradual fragmentation and transformation
  • fig. 1 From fig. 1 one can see that within the cooling rate range of rail head after hot rolling from 0.2. to 1.0°C/s, bainite and small amounts of martensite are formed in the steel structure.
  • Structure under the rail 60E1 running surface, made of steel according to the invention, is presented in fig. 3, mechanical properties are given in table 2 and hardness distribution HB within rail cross-section is presented in fig. 4.
  • Mierostructure includes around 6% of allotrimorphic ferrite, the rest is granular bainite and degenerated upper bainite. Fraction of retained austenite in the structure, determined using x-ray method is 18%.
  • Fig. 5 presents an example of TIC nano-particles precipitated in basnific ferrite.
  • Fig. 2 Relationship between austenite grain size and strain and deformation temperature. Before deformation, samples were held at temperature 1200°C for 10 minutes and the rate of deformation was critical deformation to Initiate
  • DQ initial austenite grain size (mean linear intercept) and ⁇ strain rate.
  • TIC nano-pariicies in the steel being the subject of invention observed using high resolution transmission electron microscopy, (a) --- bright field image; (b) - electron diffraction with indicated reflexes from TIC; (c) - high-resolution transmission micrograph with indicated TiC. particles.
  • Fig. 5 Distribution of HB hardness in rail cross-section of rail made of steel according to the invention.
  • Sample taken from 80E1 rail head was subject to wear process using an apparatus according to own design (fig.6). The following test conditions were applied:
  • sample from pearlstic steel grade R280 was also subject to wear test.
  • the degree of wear of this sample, under given conditions, was around 50% higher comparing to the multi
  • Fig. 6 Schematic picture of the apparatus used for wear investigation.
  • Fig. 7 presents structure of the sample of 1 steel after the wear test As can be seen, the subsurface region is subject to strong plastic deformation. Deformed retained austenitic fibres are getting aligned parallel to the surface and afterwards they are fragmented. The EBSD examination shows that the described processes are accompanied by gradual transformation of austenite to martenstte, fig. 8. However, the retained martensite is still resent in the severely deformed surface area.
  • Fig. 7 Microsiructure of the sample in the sub-surface area of the test sample, S.EM.
  • Fig. 8 Distribution of ferrite and retained ' austenite in the sample after wear test. Areas of retained austenite are presented in green and bainitic ferrite in red.
  • Table 3 shows chemical composition of manufactured multi-phase steel according to the invention and table 4 presents relevant mechanical properties of the 60E1 rail
  • Table 5 shows chemical composition of manufactured multi-phase steel according to the invention and table 6 presents mechanical properties.
  • Table 7 shows chemical composition of manufactured multi-phase steel according to the invention and table 8 presents mechanical properties.
  • Table 9 shows chemical composition of manufactured multi-phase steel according to the invention and table 10 presents mechanical properties.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Articles (AREA)

Abstract

L'invention porte sur de l'acier multiphasique utilisé pour la production de rails de voie normale, caractérisé en ce que la teneur en éléments de base dans l'acier n'est pas inférieure à 0,15 % en poids de C, 0,60 % en poids de Si, 1,20 % en poids de Mn, 1,20 % en poids de Cr, 0,20 % en poids de Ni, 0,10 % en poids de Mo, et en ce que l'acier multiphasique contient en outre de 0,01 à 0,25 % en poids de Ti, avec (% en poids de Mo)/(% en masse de Ti) > 1 ; de 0,01 à 0,80 % en poids d'Al ; de 0,001 à 0,003 % en poids de B, H2 ≤ 2 ppm, N ≤ 80 ppm, le volume des constituants individuels étant exprimé par rapport au poids total de l'acier multiphasique.
PCT/PL2016/000155 2016-06-27 2016-12-23 Acier multiphasique, en particulier pour la fabrication de rails de voie normale Ceased WO2018004363A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
US16/312,528 US20190226062A1 (en) 2016-06-27 2016-12-23 Multi-phase steel especially for production of standard-gauge rails
EP16907462.2A EP3500688A4 (fr) 2016-06-27 2016-12-23 Acier multiphasique, en particulier pour la fabrication de rails de voie normale

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
PLP.417742 2016-06-27
PL417742A PL234098B1 (pl) 2016-06-27 2016-06-27 Stal wielofazowa zwłaszcza do produkcji szyn normalnotorowych

Publications (1)

Publication Number Publication Date
WO2018004363A1 true WO2018004363A1 (fr) 2018-01-04

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ID=60786486

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/PL2016/000155 Ceased WO2018004363A1 (fr) 2016-06-27 2016-12-23 Acier multiphasique, en particulier pour la fabrication de rails de voie normale

Country Status (4)

Country Link
US (1) US20190226062A1 (fr)
EP (1) EP3500688A4 (fr)
PL (1) PL234098B1 (fr)
WO (1) WO2018004363A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108546873A (zh) * 2018-04-17 2018-09-18 包头钢铁（集团）有限责任公司 高耐磨性钢板和高耐磨性钢板的制造方法

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH02133544A (ja) 1988-11-14 1990-05-22 Nkk Corp 耐焼割れ性に優れたレール鋼
WO2004048618A1 (fr) * 2002-11-19 2004-06-10 Industeel Creusot Procede pour fabriquer une tole en acier resistant a l'abrasion et tôle obtenue
JP2009221909A (ja) 2008-03-14 2009-10-01 Nippon Steel Corp コモンレールの製造方法および部分強化されたコモンレール
EP2365103A1 (fr) * 2008-10-31 2011-09-14 Usui Kokusai Sangyo Kaisha Limited Pièce usinée en acier à haute résistance et procédé de fabrication de celle-ci, ainsi que procédé de fabrication de conduit d'injection de carburant et de rail commun pour moteur diesel

Family Cites Families (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR2840628B1 (fr) * 2002-06-05 2004-08-13 Cogifer File de rail comportant un element d'appareil de voie et un troncon de rail soudes sans apport de matiere
CZ14602U1 (cs) * 2004-06-22 2004-08-16 Dtávýhybkárnaáaámostárnaáa@Ás Ocel pro odlitky srdcovek železničních a tramvajových výhybek
CN103966520B (zh) * 2014-05-08 2016-07-06 攀钢集团攀枝花钢铁研究院有限公司 一种含有微量碳化物的贝氏体钢轨及其生产方法

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH02133544A (ja) 1988-11-14 1990-05-22 Nkk Corp 耐焼割れ性に優れたレール鋼
WO2004048618A1 (fr) * 2002-11-19 2004-06-10 Industeel Creusot Procede pour fabriquer une tole en acier resistant a l'abrasion et tôle obtenue
JP2009221909A (ja) 2008-03-14 2009-10-01 Nippon Steel Corp コモンレールの製造方法および部分強化されたコモンレール
EP2365103A1 (fr) * 2008-10-31 2011-09-14 Usui Kokusai Sangyo Kaisha Limited Pièce usinée en acier à haute résistance et procédé de fabrication de celle-ci, ainsi que procédé de fabrication de conduit d'injection de carburant et de rail commun pour moteur diesel

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
K. W. ANDREWS, J. IRON AND STEEL INST., vol. 203, 1965, pages 721 - 729
See also references of EP3500688A4

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108546873A (zh) * 2018-04-17 2018-09-18 包头钢铁（集团）有限责任公司 高耐磨性钢板和高耐磨性钢板的制造方法

Also Published As

Publication number Publication date
PL234098B1 (pl) 2020-01-31
EP3500688A4 (fr) 2020-11-11
EP3500688A1 (fr) 2019-06-26
US20190226062A1 (en) 2019-07-25
PL417742A1 (pl) 2018-01-03

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