WO2013079438A1 - Aciers pour rails avec excellente combinaison de propriétés d'usure, de résistance à la fatigue en contact roulant et de soudabilité - Google Patents

Aciers pour rails avec excellente combinaison de propriétés d'usure, de résistance à la fatigue en contact roulant et de soudabilité Download PDF

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Publication number
WO2013079438A1
WO2013079438A1 PCT/EP2012/073606 EP2012073606W WO2013079438A1 WO 2013079438 A1 WO2013079438 A1 WO 2013079438A1 EP 2012073606 W EP2012073606 W EP 2012073606W WO 2013079438 A1 WO2013079438 A1 WO 2013079438A1
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Prior art keywords
rail
steel
steel according
content
vanadium
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PCT/EP2012/073606
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English (en)
Inventor
Howard Martin Smith
Shreekant Jaiswal
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Tata Steel UK Ltd
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Tata Steel UK Ltd
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Application filed by Tata Steel UK Ltd filed Critical Tata Steel UK Ltd
Priority to EP12791480.2A priority Critical patent/EP2785890B1/fr
Priority to DK12791480.2T priority patent/DK2785890T3/en
Priority to BR112014012660-7A priority patent/BR112014012660B1/pt
Priority to PL12791480T priority patent/PL2785890T3/pl
Priority to ES12791480.2T priority patent/ES2545659T3/es
Priority to JP2014542876A priority patent/JP6270730B2/ja
Publication of WO2013079438A1 publication Critical patent/WO2013079438A1/fr
Anticipated expiration legal-status Critical
Priority to MA37151A priority patent/MA35745B1/fr
Ceased legal-status Critical Current

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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
    • C22C38/02—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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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

Definitions

  • This invention relates to a rail steel, particularly for use as a grooved rail such as those used for tramway track, having an excellent combination of properties, in particular, the resistance to both wear and rolling contact fatigue and at the same time being capable of being weld restored without the need for high temperature preheat.
  • RCF Rolling Contact Fatigue
  • composition of the new rail steel needs to be designed to not only meet the requirements of resistance to wear, RCF, and corrugation but also to ensure that the transformation to martensite occurs over such a range that it prevents completion of transformation when using the low preheat weld restoration technology.
  • the critical success factor for such a weld restoration process is the absence of any hard brittle m icrostructure or incipient cracks within the weld metal, weld metal-parent rail interface, or within the heat affected zone, all of which would subsequently lead to spalling of the deposit from the propagation of the incipient cracks through fatigue.
  • Carbon is the most cost effective strengthening alloying element in rail steels as it provides the most cost effective addition to achieve the hardness and strength in fully pearlitic steels.
  • the maximum value of carbon is 0.8%. This reduces the risk of formation of a cementite network at the grain boundaries. More preferably the range of carbon content is from 0.735% to 0.785%. This range provides the optimal balance between the volume fraction of hard cementite and the prevention of the formation of a deleterious network of embrittling cementite at grain boundaries.
  • Carbon is also a potent hardenability agent that facilitates a lower transformation temperature and hence finer interlamellar spacing.
  • the high volume fraction of hard cementite and fine interlamellar spacing provides the wear resistance and contributes towards the increased RCF resistance of the composition included in an embodiment of the invention. Furthermore, as demonstrated by the Tata Steel low preheat weld restoration process 1 , it is essential to lower the Martensite Start (Ms) temperature of the steel to ensure a robust weld deposit.
  • Ms Martensite Start
  • the prescribed range of carbon is essential to achieve this objective.
  • the following widely accepted methodologies for the calculation of M s temperature clearly identify the efficacy of carbon in reducing the magnitude of this parameter. In effect, carbon is between 13 to 17 times more potent in reducing the M s temperature compared to manganese. According to Andrews (J. Iron & Steel Inst., 183 (1965), pp.
  • M s Temperature in °C is given by 539 - 423 x % Carbon - 30.4 x % Mn (eq. 1a) and according to Steven and Haynes (J. Iron & Steel Inst., 183 (1956), pp. 349-359) by 561 - 474 x % Carbon - 33 x % Mn (eq. 1b). Both regression equations provide slightly different values for M s . In the context of this invention the average value of these two equations was used as a the approximation of the actual M s . M f is then determined from M s by subtracting 150°C from M s .
  • M s (°C) 0.5 X (M s , Andrews + M s , stevens&Haynes) ⁇ eq . 1>
  • the Martensite Start (M s ) temperature of the steel is below about 160°C to ensure a robust weld deposit.
  • the addition of Silicon is an integral and essential part of the design of the steel to engineer the resulting microstructure and properties and not, as in most other rail steels, a reflection of the manufacturing process route rather than an intentional alloying addition. Silicon is often used as a deoxidising element and as such the addition of silicon is usually intended for that purpose only.
  • the microstructure contains little or no proeutectoid ferrite. Instead it is primarily the interlamellar spacing of the pearlite that dictates the resulting properties.
  • the refinement of the pearlitic microstructure in grooved rail compositions has been achieved through the use of accelerated cooling.
  • the novelty of the approach in this invention is to treat the pearlitic microstructure as a three-dimensional entity in which the behaviour at the wheel-rail interface is governed by the properties of the two components of pearlite, ferrite and cementite laths, rather than just the bulk properties of hardness and tensile strength. Consequently, the novelty in this invention lies in the use of silicon to strengthen the pearlitic ferrite through solid solution strengthening which in turn imparts an increased resistance to ratchetting, wear, and rolling contact fatigue. A minimum Silicon content of 0.65% is essential for the steel according to the invention to attain the required mechanical property values, wear resistance and RCF resistance.
  • Silicon additions have a very limited effect on hardenability of steel and this is reflected in the equations for the calculation of M s temperature, the addition of up to 1.0% Silicon is acknowledged to make a small contribution to the lowering of the M s temperature. Silicon content between 0.65% and 0.80% was found to provide a good balance of the required mechanical properties without any adverse effect on weld restorability.
  • Manganese is a key alloying element in all grooved rail steels to provide the required hardenability to ensure a relatively fine interlam el lar spacing following natural or accelerated cooling of such steels. This purpose remains valid for the current invention. In the current invention, which does not rely on accelerated cooling for its properties, a higher manganese content is considered desirable to impart sufficient hardenability to achieve a pearlitic microstructure with fine interlamellar spacing. A manganese content of less than 1.1 %Mn was found to be insufficient to achieve the desired hardenability at the chosen carbon content while at levels above 1.4%, the increased risk of formation of martensite, particularly in areas of segregation of manganese, was considered unacceptable.
  • a higher level of manganese is also considered undesirable from a welding perspective because of the increased risk of formation of hard and embrittling martensite.
  • the manganese content is at most 1.35%.
  • a suitable minimum value for the manganese would be 1.20% or even 1.25%.
  • vanadium as a precipitation strengthening alloying element has been utilised in this invention to strengthen the pearlitic ferrite and thereby increase the resistance to ratchetting, wear, and rolling contact fatigue.
  • Vanadium forms vanadium carbides or vanadium nitrides depending on the amount of nitrogen present in the steel and the temperature. Therefore, it is necessary to examine the level of vanadium addition together with the magnitude of nitrogen in the steel as the efficacy of precipitation strengthening in eutectoid pearlitic steels decreases with increasing levels of nitrogen, which leads to coarser precipitates of vanadium nitride at higher temperatures.
  • minimum nitrogen content of 0.003% is considered a practical lower limit while a higher limit of 0.007% is considered desirable to ensure best returns from the additions of costly vanadium.
  • higher nitrogen contents could be tolerated provided they are accompanied by proportionately higher vanadium contents.
  • the minimum amount of nitrogen is 0.003% coupled with minimum vanadium content of 0.07%.
  • nitrogen is at most 0.007% while the corresponding figures for vanadium are 0.07% minimum and 0.12% maximum. Although these maximum contents could be exceeded, they are non-ideal and economically unattractive.
  • the phosphorus content of the steel is at most 0.015%.
  • Suphur values must be between 0.008 and 0.030% because it forms MnS inclusions. These inclusions act as sinks for any residual hydrogen that may be present in the steel. This hydrogen can result in shatter cracks which can be the initiators of fatigue cracks in the head (also known as tache ovals) under the high stresses from the wheels.
  • the addition of at least 0.008% sulphur prevents the deleterious effects of hydrogen, whereas a maximum value of 0.03% is chosen to avoid embrittlement of the structure.
  • the maximum value is 0.025%.
  • Boron although not a mandatory alloying element, could be used to improve the properties of the steel according to the invention and amounts up to about 60 ppm could be used. Boron is a strong promoter of the formation of m icrostructural components such as bainite or martensite, particularly when the nitrogen in the steel is bound by titanium. If not, BN-precipitates may be formed.
  • the microstructure is substantially pearlitic and preferably fully pearlitic and that the amount of bainitic or martensitic microstructural components is kept as low as possible and preferably are absent.
  • the maximum recommended level of unavoidable impurities are based on EN13674-1:2003, according to which the maximum limits are Mo 0.02%, Ni 0.10%, Sn - 0.03%, Sb - 0.020%, Ti - 0.025%, Nb - 0.01%.
  • test conditions for wear testing involve the use of a 560 MPa contact stress and 25% slip while those for RCF utilise a higher contact stress of 900 MPa, 5% slip and water lubrication.
  • the results are shown in Figure 1 where the wear rate in mg/m slip is plotted against the hardness (in HV).
  • Silicon is a solid solution strengthener and increases the strength of the pearlitic ferrite, thereby increasing the resistance of the pearlite to both wear and RCF initiation.
  • the precipitation of fine vanadium carbides within the pearlitic ferrite increases its strength, in particular the proof strength, and thereby the resistance to both wear and RCF.
  • a further feature of the compositional design is to limit the nitrogen content in order to prevent the premature formation of relatively coarse precipitates of vanadium nitride, as they are significantly less effective in increasing the strength of the pearlitic ferrite. This ensures that the vanadium additions remain in solution within the austenite to lower temperatures and, therefore, result in finer precipitates.
  • a proportion of the vanadium also remains in solution, thereby acting as a hardenability agent to refine the pearlite spacing.
  • the specific design of the composition claimed in this embodiment utilises the various attributes of the individual elements to produce a microstructure with a highly desirable combination of wear and RCF resistance.
  • the mechanical properties and the resistance to both wear and RCF initiation of the steels in accordance with the invention are better than most conventional heat treated pearlitic rail grades and similar to the hardest heat treated grade (Grade R340GHT) included in the Euro norm for grooved rails (EN 14811 :2006 + A1 : 2009).
  • Another and equally significant additional attribute of the steels in accordance with the invention is their ability to be weld restored without the need for high temperature preheat.
  • the proprietary Tata Steel weld restoration process specifies low preheat temperatures of about 60°C to 80°C.
  • the fundamental principle on which this process is based is the avoidance of the completion of transformation to martensite within the heat affected zone created by the deposited weld bead.
  • the design of the steel composition has had two challenging objectives: firstly to meet the property requirements described in preceding paragraphs and secondly to ensure the martensite start (M s ) and martensite finish (M f ) transformation temperatures are such that they do not permit the transformation to martensite to go to completion during the weld restoration process.
  • the M f temperature needs to be below about 60°C and preferably much below this temperature to maximise the volume of untransformed retained austenite that is key to the prevention of the formation of incipient cracks at the weld- parent metal interface or within the heat affected zone formed by the deposition of the weld bead.
  • the M f temperature is considered to be about 150°C below the M s temperature which can be calculated using the equations (1), (1a), (1b) and (2) as given above.
  • the M s and M f tern perature of a range of rail steels available is shown in Figure 2 against the required minimum hardness of the grade.
  • the temperatures are the average of those calculated by the two equations given in paragraph 0012 and the concentrations of carbon and manganese used in the calculations are the midpoint values of the range specified in EN 14811 :2006 +A1: 2009.
  • the M s temperature is the upper value
  • the M f temperature is the lower value of the depicted range.
  • the steel of this invention referenced as "Invention" in figure 2
  • the steel of this invention has the lowest M f temperature and hence is capable of retaining the maximum proportion of austenite and therefore most resistant to the formation of incipient cracks.
  • the other grooved rail steel grades have undesirably higher M f temperatures implying completion of martensite transformation during weld restoration and a much higher risk of the formation of cracks.
  • the excellent wear resistance of the rail ensures that it takes a long time before the rail is worn down in a vertical direction.
  • the weld restorability and the fact that the steel according to the invention does not require a heat treatment to achieve its properties ensures that the rail can be repaired in situ, so the rail does not have to be taken out of the street but can be repaired overnight. This involves less road works and less inconvenience for inner city traffic.
  • This combination of properties achievable by engineering the microstructure and the chemistry of the rail means that the rail is not only cost effective, but also provides a more ecological solution because rails can be easily repaired and do not have to be replaced by new rails as often.
  • careful compositional design thereby eliminating the need for a heat treatment step during rail manufacture, also ensures a greener rail product in comparison with steels which derive their properties from a heat treatment after rolling the rail.
  • the steel according to the invention is suitable for purposes such as crane rails or flat-bottomed rails, it has been found that the rail steel is exceptionally suitable for the production of grooved rails that benefit from the combined key attributes of wear resistance and weld restorability.
  • a 300 t commercial BOS cast (steel B) was produced of the inventive steel based on the chemistry of lab cast A, and subsequently continuously cast to a 355 x 305 mm bloom section.
  • the blooms were rolled to various rail sections and were allowed to cool on the rail cooling bank under the standard cooling conditions as for conventional as-rolled commercial rail grades. All rail lengths were produced free from any internal or surface breaking defects. The rails were tested in the as-hot-rolled condition.
  • the hardness of the steels A and B was found to be between 330 and 335 HV30.
  • the inventors found that by selecting a steel in the narrow chemistry window in accordance with the invention that both wear resistance and RCF resistance are excellent and match the performance of a heat treated Grade 350HT whilst showing similar mechanical properties. In comparison to some grades our inventive steels do not require heat treatment to obtain the desired properties.
  • Table 2 Hardness & tensile property data for the inventive steels and current pearlitic rail grades (R260 and R350HT).

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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 Articles (AREA)

Abstract

L'invention concerne un acier destiné à la fabrication de rails, en particulier de rails à gorge, présentant une dureté d'au moins 330 HV30, une résistance à la traction d'au moins 1000 MPa et une limite élastique d'au moins 600 Mpa et comportant en % de poids : 0,70% à 0,85% de carbone ; 0,65% à 1,00% de silicium ; 1,1% à 1,4% de manganèse ; 0,07% à 0,15% de vanadium ; jusqu'à 0,008% d'azote ; jusqu'à 0,025% de phosphore ; 0,008% à 0,030% de soufre ; au plus 2,5 ppm d'hydrogène ; au plus 0,10% de chrome ; au plus 0,010% d'aluminium ; au plus 20 ppm d'oxygène ; le reste étant constitué de fer et d'impuretés inévitables.
PCT/EP2012/073606 2011-11-28 2012-11-26 Aciers pour rails avec excellente combinaison de propriétés d'usure, de résistance à la fatigue en contact roulant et de soudabilité Ceased WO2013079438A1 (fr)

Priority Applications (7)

Application Number Priority Date Filing Date Title
EP12791480.2A EP2785890B1 (fr) 2011-11-28 2012-11-26 Aciers pour rails avec excellente combinaison de propriétés d'usure, de résistance à la fatigue en contact roulant et de soudabilité
DK12791480.2T DK2785890T3 (en) 2011-11-28 2012-11-26 RAIL STEEL WITH A UNIQUE COMBINATION OF WEAR PROPERTIES OF FATIGUE STRENGTH BY ROLLER CONTACT AND weldability
BR112014012660-7A BR112014012660B1 (pt) 2011-11-28 2012-11-26 aço para a fabricação de trilhos e trilho
PL12791480T PL2785890T3 (pl) 2011-11-28 2012-11-26 Stal szynowa o doskonałej kombinacji odporności na zużycie, na zmęczenie toczne i spawalności
ES12791480.2T ES2545659T3 (es) 2011-11-28 2012-11-26 Acero para raíles con una excelente combinación de propiedades de desgaste, resistencia a la fatiga de contacto por rodadura y soldabilidad
JP2014542876A JP6270730B2 (ja) 2011-11-28 2012-11-26 耐摩耗性、転がり接触疲労耐性および溶接性の優れた組み合わせを有するレール鋼
MA37151A MA35745B1 (fr) 2011-11-28 2014-06-25 Aciers pour rails avec excellente combinaison de propriétés d'usure, de résistance à la fatigue en contact roulant et de soudabilité

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
EP11190973.5 2011-11-28
EP11190973 2011-11-28

Publications (1)

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WO2013079438A1 true WO2013079438A1 (fr) 2013-06-06

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PCT/EP2012/073606 Ceased WO2013079438A1 (fr) 2011-11-28 2012-11-26 Aciers pour rails avec excellente combinaison de propriétés d'usure, de résistance à la fatigue en contact roulant et de soudabilité

Country Status (10)

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EP (1) EP2785890B1 (fr)
JP (1) JP6270730B2 (fr)
BR (1) BR112014012660B1 (fr)
DK (1) DK2785890T3 (fr)
ES (1) ES2545659T3 (fr)
HU (1) HUE027275T2 (fr)
MA (1) MA35745B1 (fr)
PL (1) PL2785890T3 (fr)
PT (1) PT2785890E (fr)
WO (1) WO2013079438A1 (fr)

Cited By (3)

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Publication number Priority date Publication date Assignee Title
CN105112786A (zh) * 2015-09-29 2015-12-02 燕山大学 一种超级珠光体钢轨钢及其制备方法
AU2015205937B2 (en) * 2014-09-02 2016-07-28 Pangang Group Panzhihua Iron & Steel Research Institute Co., Ltd. Pearlitic steel rail with high strength and toughness and producing method thereof
CN108431265A (zh) * 2015-12-15 2018-08-21 杰富意钢铁株式会社 钢轨钢及车轮钢的选择方法

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US4895605A (en) * 1988-08-19 1990-01-23 Algoma Steel Corporation Method for the manufacture of hardened railroad rails
US5830286A (en) * 1995-03-14 1998-11-03 Nippon Steel Corporation Steel rail having excellent wear resistance and internal breakage resistance, and method of producing the same
US5899516A (en) * 1996-01-23 1999-05-04 Sumitomo Metal Industries, Ltd. Railway wheel and manufacturing method of the railway wheel
WO2002008482A1 (fr) * 2000-07-21 2002-01-31 Transportation Technology Center, Inc. Roues de chemin de fer resistant a une transformation martensitique
EP1241277A2 (fr) * 2001-03-05 2002-09-18 AMSTED Industries Incorporated Alliage de roue ferroviaire
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ES2545659T3 (es) 2015-09-14
DK2785890T3 (en) 2015-08-24
EP2785890B1 (fr) 2015-07-15
PL2785890T3 (pl) 2015-12-31
MA35745B1 (fr) 2014-12-01
HUE027275T2 (en) 2016-10-28
BR112014012660A2 (pt) 2017-06-13
PT2785890E (pt) 2015-10-01
BR112014012660B1 (pt) 2018-12-04

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