EP3821040A1 - Partie de voie en acier hypereutectoïde - Google Patents
Partie de voie en acier hypereutectoïdeInfo
- Publication number
- EP3821040A1 EP3821040A1 EP19752261.8A EP19752261A EP3821040A1 EP 3821040 A1 EP3821040 A1 EP 3821040A1 EP 19752261 A EP19752261 A EP 19752261A EP 3821040 A1 EP3821040 A1 EP 3821040A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- rail
- track part
- hypereutectoid steel
- amount
- part according
- 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.)
- Granted
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 49
- 239000010959 steel Substances 0.000 title claims abstract description 49
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical group C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 claims abstract description 51
- 229910001567 cementite Inorganic materials 0.000 claims abstract description 50
- 238000004458 analytical method Methods 0.000 claims abstract description 9
- 238000001816 cooling Methods 0.000 claims description 19
- 238000000034 method Methods 0.000 claims description 18
- 238000005096 rolling process Methods 0.000 claims description 12
- 239000000203 mixture Substances 0.000 claims description 11
- 238000004519 manufacturing process Methods 0.000 claims description 5
- 239000002826 coolant Substances 0.000 claims description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 3
- 229920000642 polymer Polymers 0.000 claims description 2
- 230000000052 comparative effect Effects 0.000 claims 1
- 229910052799 carbon Inorganic materials 0.000 description 22
- 239000002244 precipitate Substances 0.000 description 15
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 14
- 229910052710 silicon Inorganic materials 0.000 description 11
- 239000011651 chromium Substances 0.000 description 9
- 229910052748 manganese Inorganic materials 0.000 description 9
- 239000011572 manganese Substances 0.000 description 9
- 239000010955 niobium Substances 0.000 description 9
- 229910052804 chromium Inorganic materials 0.000 description 8
- 238000001556 precipitation Methods 0.000 description 8
- 229910052720 vanadium Inorganic materials 0.000 description 8
- 230000000694 effects Effects 0.000 description 7
- 238000010438 heat treatment Methods 0.000 description 7
- 235000019362 perlite Nutrition 0.000 description 7
- 239000010451 perlite Substances 0.000 description 7
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 6
- 229910045601 alloy Inorganic materials 0.000 description 6
- 239000000956 alloy Substances 0.000 description 6
- 230000015572 biosynthetic process Effects 0.000 description 6
- 230000006378 damage Effects 0.000 description 6
- 239000000463 material Substances 0.000 description 6
- 229910052758 niobium Inorganic materials 0.000 description 6
- 230000008569 process Effects 0.000 description 6
- 239000010703 silicon Substances 0.000 description 6
- 239000011573 trace mineral Substances 0.000 description 6
- 235000013619 trace mineral Nutrition 0.000 description 6
- 229910001566 austenite Inorganic materials 0.000 description 5
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 4
- 229910052782 aluminium Inorganic materials 0.000 description 4
- 229910001562 pearlite Inorganic materials 0.000 description 4
- 230000001629 suppression Effects 0.000 description 4
- 229910052719 titanium Inorganic materials 0.000 description 4
- 239000010936 titanium Substances 0.000 description 4
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 3
- 238000005275 alloying Methods 0.000 description 3
- 238000011161 development Methods 0.000 description 3
- 238000012423 maintenance Methods 0.000 description 3
- 230000007704 transition Effects 0.000 description 3
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 230000017525 heat dissipation Effects 0.000 description 2
- QMQXDJATSGGYDR-UHFFFAOYSA-N methylidyneiron Chemical compound [C].[Fe] QMQXDJATSGGYDR-UHFFFAOYSA-N 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 241000446313 Lamella Species 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 229910052787 antimony Inorganic materials 0.000 description 1
- 229910052785 arsenic Inorganic materials 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 230000006735 deficit Effects 0.000 description 1
- 230000001627 detrimental effect Effects 0.000 description 1
- 238000005530 etching Methods 0.000 description 1
- 238000001704 evaporation Methods 0.000 description 1
- 230000008020 evaporation Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 229910052745 lead Inorganic materials 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 230000008092 positive effect Effects 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000009528 severe injury Effects 0.000 description 1
- 230000011664 signaling Effects 0.000 description 1
- 238000004901 spalling Methods 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 238000010186 staining Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
- 238000012546 transfer Methods 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
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
- C22C38/18—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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/08—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling structural sections, i.e. work of special cross-section, e.g. angle steel
- B21B1/085—Rail sections
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
- C21D1/60—Aqueous agents
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/62—Quenching devices
- C21D1/63—Quenching devices for bath quenching
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
-
- 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
- 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
-
- 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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- 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
- C21D2211/003—Cementite
-
- 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
- C21D2211/009—Pearlite
-
- 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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
Definitions
- the invention relates to a track part, in particular a rail for rail vehicles, made of a hypereutectoid steel
- the invention further relates to a method for producing such a track part.
- RCF surface damage examples are e.g. head checks
- Hypereutectoid steels are known for producing rails, for example from EP 2388352 A1.
- the iron-carbon diagram shows an eutectoid at a carbon content (C content) of 0.77% by weight of carbon and at a temperature of 723 °C, at which point a fixed direct phase transition from the austenite phase to the perlite phase occurs on cooling.
- Perlite is preferred over other steel modifications for rails in terms of wear resistance and elongation at break, as it is best for wear due to the lamellar structure.
- the pearlitic structure comprises a ferrite phase, wherein the ferrite content in the perlite phase can be regarded as a tough and ductile phase and as a fixed variable, because the C-content of the rail steel varies only in very narrow limits, and the pearlitic structure further comprises a cementite phase, wherein the ferrite and the cemetite phases are arranged in lamellar
- secondary cementite precipitates are significantly influenced by a combination of alloying and heat treatment technology.
- the knowledge of the precipitation temperature of the secondary cementite is of crucial importance and one should not fall below the precipitation temperature before the subsequent heat treatment.
- the cooling rate during the heat treatment process should be as high as possible to suppress the precipitation of secondary cementite.
- Essential for the quality of a rail is thus a high wear resistance, for which essentially the hardness (for example indicated as Brinell hardness) of the rail is
- the desirable hardness inevitably goes hand in hand with a reduction in toughness, which is detrimental to the durability of the track part, especially in heavy load, where the rail is subjected to particularly high bending stresses when driving over a rail vehicle.
- the invention therefore aims to improve a track part, in particular a rail, which is to consist of a low-alloy steel for reasons of cost and ease of welding, to the effect that due to a high hardness of the material even at elevated wheel loads, the wear resistance in the rail head is increased so far that a use time of longer than 30 years can be ensured.
- the track part should be well weldable and have similar other material properties as proven steels used in the rail construction, such as e.g. a similar electrical conductivity and a similar coefficient of thermal expansion.
- the invention aims to provide a simple
- the manufacturing method for a track part according to the invention which is characterized by a short process time (avoidance of incandescent phases) , high reproducibility and high cost-effectiveness.
- the method shall be suitable for producing long rails of e.g. over 100 m in length, with specification-compliant material properties over the entire rail length to be ensured.
- the invention according to a first aspect provides a track part, in particular a rail of the type mentioned above, which is characterized in that a hypereutectoid steel with the following directional
- o of Cr and the steel, at least in the head portion of the rail, has a pearlitic structure that is substantially free of secondary cementite networks.
- the rail according to the invention has proven to be extremely suitable, since a hardness in the range of 460 HB and higher could be achieved and the rail according to the invention at the same time has a sufficient elongation at break for the heavy load range.
- a secondary cementite network means a microstructure in which the former austenite grains are completely surrounded by a closed network of secondary cementite .
- Secondary cementite precipitates reduce the carbon supply for the formation of pearlitic cementite lamellae needed for wear resistance. For these reasons, the suppression of secondary cementite in hypereutectoid rail steels is considered to be advantageous.
- the concentration of manganese in the present steel is selected to shift the formation of embrittling secondary cementite to lower temperatures due to its austenite stabilizing effect, thereby enabling fine grain rolling at low rolling temperatures of hypereutectoid rail steels while suppressing secondary cementite precipitation.
- the lower limit of 0.9 wt.-% manganese was chosen because the precipitation temperature of embrittling secondary cementite shifts to higher temperatures if one falls below this lower limit, which would result in that the
- the upper limit of 1.35 wt.-% manganese was chosen to ensure castability of the steel.
- the alloy composition of the present invention provides a lower limit of the carbon content of 0.98 wt% and an upper limit of 1.17 wt%.
- the lower limit was chosen here in view of a sufficient strength, since carbon brings the required strength.
- the upper limit was chosen in order to avoid the precipitation of secondary cementite networks, especially from a depth of approx. 5-10 mm below the rail head
- the alloy composition of the invention provides for silicon a lower limit of 0.70 wt.-% and an upper limit of 1.10 wt . - %.
- the lower limit was chosen to ensure the effectiveness of silicon to suppress embrittling secondary cementite precipitates. This extends the process window of the heat treatment so that a secondary cementite network can be avoided.
- the upper limit is based on the background that, if this limit is exceeded, the required electrical
- the alloy composition according to the invention provides for chromium a lower limit of 0.15 wt.-% and an upper limit of 0.70 wt.-%. It has been found that chromium, starting at a content of 0.15 wt.-%, has a marked effect on the cross- section hardening of the rail and suppresses the formation of secondary cementite, which in turn widens the process window of the heat treatment, so that the secondary
- cementite structure cannot be formed as a network.
- the upper limit of 0.70 wt.-% was chosen because the
- weldability of the rail is made difficult or impossible with increasing chromium content.
- the invention is based on a particular selection of the quantitative ranges of the individual alloy constituents, the individual alloying constituents having partially opposite effects.
- a higher carbon content is desirable for achieving high strengths, but as the carbon content increases, the disadvantage of the increasing austenite-to-perlite- transition temperature has to be considered.
- high silicon contents are responsible for the suppression of embrittling secondary cementite precipitates, they also increases the austenite-to-perlite-transition temperature.
- secondary cementite precipitates at relatively high temperatures due to the relatively high carbon and silicon content, so that secondary cementite precipitates can occur in an enhanced form also prior to the heat treatment process.
- the use of high carbon content in combination with silicon is actually counterproductive.
- high silicon concentrations also have a diffusion- inhibiting effect on carbon and thus minimize secondary cementite. To take advantage of this positive effect, the negative effect of the shift in the transformation
- the directional analysis of the rail steel may be formed such that A1 (aluminum) is additionally used in amounts of 0.01- 0.06 wt.-%. This leads to a minimization of the pearlite grain size, which is beneficial to the elongation at break.
- vanadium may additionally be used in amounts of from 0.07 to 0.20 wt.-%, in particular from 0.10 to 0.20 wt.-%, as in a preferred embodiment of the present invention. It has been found that already starting from a vanadium content of 0.07 wt.-%, an increase in strength and a grain refining effect may be achieved. The strength decreases again from the upper limit of 0.2 wt.-%, since too much C from the matrix is bound.
- Nb niobium
- Nb niobium
- (titanium) may additionally be used in amounts of 0.015 - 0.05 wt . -% .
- V is used in amounts of 0.07 to 0.20 wt.-%, in particular 0.10 to 0.2 wt.-%, together with Nb in amounts of 0.010 to 0.030 wt.-%.
- Al is used in amounts of 0.01 - 0.06 wt.-% together with Nb in amounts of 0.01 - 0.03 wt.-%.
- the grain refining effect can be increased by a nitrogen content set in the steel in the range of 40 to 120 ppm, which corresponds to a preferred embodiment of the present invention.
- a steel quality is achieved which enables the production of a track part in which the steel, at least in the head portion of the rail, has a tensile strength greater than 1500 MPa, an elongation at break of greater than 8% and a Brinell hardness (according to EN ISO 6506-1) of greater than 460 HB, as corresponds to a
- the inventive method for producing a track part according to the invention is characterized in that a hypereutectoid steel having a composition according to any one of claims 1 to 9 is taken from a furnace at a temperature of 1000 - 1300°C, then rolled at a final rolling temperature of 850 - 950°C and is then subjected to forced cooling to a
- the furnace is preferably a walking beam furnace.
- the steel with the composition according to the invention is removed from the furnace and rolled to the desired shape of the track part, in
- the conditions in the rolling mill are selected by means of the accumulated degree of transformation within continuous rolling passes on the finishing scale such that a recrystallization- controlled rolling process is achieved by means of
- austenite grain size 8 pm to 35 pm, at least in the head portion of the rail. According to the invention this is followed by a rapid cooling to below 600°C, in which temperature range no secondary cementite is precipitated any more, creating a very wear-resistant fine-pearlitic microstructure with sufficient elongation at break for the heavy-duty application.
- the forced cooling takes place at least in the head portion of the rail, in order to ensure at least there the pearlitic structure.
- the cooling rate is chosen so high that a substantial suppression of secondary cementite precipitation takes place, but no formation of undesirable secondary phases such as wear-promoting bainite or martensite occurs.
- the process according to the invention is preferably further developed in that the forced cooling takes place in a bath of cooling medium not being pure water.
- cooling medium not being pure water.
- cementite precipitates to a more rapid cooling, and on the other hand, suppresses the emergence of soft staining the surface of the rail.
- a particularly effective cooling succeeds in the interest of avoiding secondary cementite precipitates, when the forced cooling takes place in a polymer bath with a temperature of 10 - 70°C, as provided according to a preferred embodiment of the present invention.
- the method is carried out such that, to avoid secondary cementite precipitates, the forced cooling is performed at a rate of at least 4°C/sec, preferably at least 8°C/sec, more preferably at least 12°C/sec. In this way, the area of the formation of secondary cementite precipitates is quickly passed through in the iron-carbon diagram, so that the embrittlement of the rail steel can be effectively avoided.
- a rail for railway vehicles was made of a hypereutectoid steel with the following directional analysis according to the method of the invention:
- Example 2 A rail for railway vehicles was made of a hypereutectoid steel with the following directional analysis according to the method of the invention:
- a rail with a tensile strength of 1550 MPa/mm 2 A rail with a tensile strength of 1550 MPa/mm 2 , an
- a rail for railway vehicles was made of a hypereutectoid steel with the following directional analysis according to the method of the invention:
- a rail for railway vehicles was made of a hypereutectoid steel with the following directional analysis according to the method of the invention:
- a rail for railway vehicles was made of a hypereutectoid steel with the following directional analysis according to the method of the invention:
- a rail with a tensile strength of 1570 MPa/mm 2 A rail with a tensile strength of 1570 MPa/mm 2 , an
- the rails produced according to Examples 1 to 5 have a purely pearlitic microstructure essentially free of
- the rail material microstructure at least in the standard tensile test position of the rail (10 mm below the running edge) , has a pearlitic structure below 3%-nital-etching substantially free of secondary cementite networks
- the cementite lamella thickness is significantly increased in the case of the rail according to the invention compared with a rail from the prior art (rail R400HT according to EN 13674-1), as can be seen from Fig. 2.
- the degree of secondary cementite itself can be assessed with the aid of a classification chart for assessing the secondary cementite precipitates on the microstructure, as shown in Fig. 3.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials 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
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
ATA201/2018A AT521405B1 (de) | 2018-07-10 | 2018-07-10 | Gleisteil aus einem hypereutektoiden Stahl |
PCT/IB2019/055660 WO2020012297A1 (fr) | 2018-07-10 | 2019-07-03 | Partie de voie en acier hypereutectoïde |
Publications (2)
Publication Number | Publication Date |
---|---|
EP3821040A1 true EP3821040A1 (fr) | 2021-05-19 |
EP3821040B1 EP3821040B1 (fr) | 2023-08-30 |
Family
ID=67551584
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP19752261.8A Active EP3821040B1 (fr) | 2018-07-10 | 2019-07-03 | Partie de voie en acier hypereutectoïde |
Country Status (13)
Country | Link |
---|---|
US (1) | US20200017943A1 (fr) |
EP (1) | EP3821040B1 (fr) |
AR (1) | AR115726A1 (fr) |
AT (1) | AT521405B1 (fr) |
AU (1) | AU2019204857A1 (fr) |
BR (1) | BR102019014230B1 (fr) |
CA (1) | CA3048723C (fr) |
ES (1) | ES2834057T3 (fr) |
MA (1) | MA53132A (fr) |
PL (1) | PL3821040T3 (fr) |
UA (1) | UA127116C2 (fr) |
WO (1) | WO2020012297A1 (fr) |
ZA (1) | ZA202006996B (fr) |
Families Citing this family (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
AU2021302317B2 (en) * | 2020-06-29 | 2023-11-16 | Jfe Steel Corporation | Rail having excellent fatigue crack propagation resistance characteristics, and method for producing same |
CN115094338B (zh) * | 2022-07-27 | 2023-09-22 | 内蒙古科技大学 | 一种过共析钢轨用钢及其制备方法 |
WO2024134872A1 (fr) * | 2022-12-23 | 2024-06-27 | 日本製鉄株式会社 | Rail et procédé de fabrication de rail |
Family Cites Families (13)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US5762723A (en) * | 1994-11-15 | 1998-06-09 | Nippon Steel Corporation | Pearlitic steel rail having excellent wear resistance and method of producing the same |
DE19906694C2 (de) | 1999-02-18 | 2002-04-11 | Lueraflex Gmbh G Lueckenotto | Breitstreckwalze |
JP2002256393A (ja) * | 2001-02-28 | 2002-09-11 | Nippon Steel Corp | 耐破壊性に優れた耐摩耗パーライト系レール |
US20040187981A1 (en) * | 2002-04-05 | 2004-09-30 | Masaharu Ueda | Pealite base rail excellent in wear resistance and ductility and method for production thereof |
JP4272410B2 (ja) * | 2002-11-12 | 2009-06-03 | 新日本製鐵株式会社 | パーライトレールの熱処理方法 |
JP4336101B2 (ja) * | 2002-12-25 | 2009-09-30 | 新日本製鐵株式会社 | 耐摩耗性および靭性に優れた高炭素パーライト系レール |
JP5145795B2 (ja) * | 2006-07-24 | 2013-02-20 | 新日鐵住金株式会社 | 耐摩耗性および延性に優れたパーライト系レールの製造方法 |
ITMI20072244A1 (it) * | 2007-11-28 | 2009-05-29 | Danieli Off Mecc | Dispositivo per trattamento termico di rotaie e relativo processo |
CN102301023B (zh) * | 2009-02-18 | 2013-07-10 | 新日铁住金株式会社 | 耐磨损性及韧性优异的珠光体系钢轨 |
BRPI1011986A2 (pt) * | 2009-06-26 | 2016-04-26 | Nippon Steel Corp | trilho de aço com alto teor de carbono com base em perlita tendo excelente ductilidade e processo para a produção deste |
JP5776565B2 (ja) * | 2012-01-23 | 2015-09-09 | 新日鐵住金株式会社 | レール鋼及び車輪鋼の材質選択方法 |
US9534278B2 (en) * | 2012-06-14 | 2017-01-03 | Nippon Steel & Sumitomo Metal Corporation | Rail |
BR112018073094A2 (pt) * | 2016-05-19 | 2019-03-06 | Nippon Steel & Sumitomo Metal Corp | trilho |
-
2018
- 2018-07-10 AT ATA201/2018A patent/AT521405B1/de active
-
2019
- 2019-07-03 WO PCT/IB2019/055660 patent/WO2020012297A1/fr active Search and Examination
- 2019-07-03 PL PL19752261.8T patent/PL3821040T3/pl unknown
- 2019-07-03 EP EP19752261.8A patent/EP3821040B1/fr active Active
- 2019-07-03 MA MA053132A patent/MA53132A/fr unknown
- 2019-07-03 UA UAA202100541A patent/UA127116C2/uk unknown
- 2019-07-03 ES ES19752261T patent/ES2834057T3/es active Active
- 2019-07-05 CA CA3048723A patent/CA3048723C/fr active Active
- 2019-07-05 AU AU2019204857A patent/AU2019204857A1/en active Pending
- 2019-07-09 US US16/506,234 patent/US20200017943A1/en not_active Abandoned
- 2019-07-09 BR BR102019014230-8A patent/BR102019014230B1/pt active IP Right Grant
- 2019-07-10 AR ARP190101938A patent/AR115726A1/es unknown
-
2020
- 2020-11-10 ZA ZA2020/06996A patent/ZA202006996B/en unknown
Also Published As
Publication number | Publication date |
---|---|
EP3821040B1 (fr) | 2023-08-30 |
ZA202006996B (en) | 2021-10-27 |
CA3048723C (fr) | 2021-11-09 |
BR102019014230B1 (pt) | 2023-10-31 |
CA3048723A1 (fr) | 2020-01-10 |
AT521405A1 (de) | 2020-01-15 |
AU2019204857A1 (en) | 2020-01-30 |
ES2834057T1 (es) | 2021-06-16 |
AR115726A1 (es) | 2021-02-17 |
UA127116C2 (uk) | 2023-05-03 |
WO2020012297A1 (fr) | 2020-01-16 |
MA53132A (fr) | 2021-05-19 |
PL3821040T3 (pl) | 2024-02-12 |
ES2834057T3 (es) | 2024-03-26 |
BR102019014230A2 (pt) | 2020-02-27 |
US20200017943A1 (en) | 2020-01-16 |
AT521405B1 (de) | 2021-09-15 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
AU2016200056B2 (en) | High-Strength and Highly Fatigue-Resistant Steel Rail and Production Method Thereof | |
JP5292875B2 (ja) | 耐摩耗性,耐疲労損傷性および耐遅れ破壊性に優れた内部高硬度型パーライト鋼レールおよびその製造方法 | |
US20170191149A1 (en) | Railway vehicle wheel and method for manufacturing railway vehicle wheel | |
JP2009108397A (ja) | 耐摩耗性と耐疲労損傷性に優れた内部高硬度型パーライト鋼レールおよびその製造方法 | |
CA3048723C (fr) | Partie de voie faite d`un acier hypereutectoide | |
JP5282506B2 (ja) | 耐摩耗性と耐疲労損傷性に優れた内部高硬度型パーライト鋼レールおよびその製造方法 | |
US8430976B2 (en) | Rail steel with an excellent combination of wear properties and rolling contact fatigue resistance | |
WO2022004247A1 (fr) | Rail présentant d'excellentes caractéristiques de résistance à la propagation de fissures par fatigue, et son procédé de production | |
JP3445619B2 (ja) | 耐摩耗性および耐内部損傷性に優れたレールおよびその製造方法 | |
EP3778961B1 (fr) | Rail, et procédé de fabrication de celui-ci | |
KR20050075033A (ko) | 용접용 강 빌딩 구성요소 및 그 제조방법 | |
JPWO2018174095A1 (ja) | レールおよびその製造方法 | |
JP4736790B2 (ja) | 高強度パーライト系レールおよびその製造方法 | |
JP6555447B2 (ja) | レールの製造方法 | |
OA20006A (en) | Track Part Made of a Hypereutectoid Steel. | |
JP3832169B2 (ja) | 耐摩耗性と延靭性に優れたパーライト鋼レールの製造方法 | |
JP6822575B2 (ja) | レールおよびその製造方法 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: UNKNOWN |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE |
|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE |
|
17P | Request for examination filed |
Effective date: 20210113 |
|
AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
REG | Reference to a national code |
Ref country code: ES Ref legal event code: BA2A Ref document number: 2834057 Country of ref document: ES Kind code of ref document: T1 Effective date: 20210616 |
|
RAV | Requested validation state of the european patent: fee paid |
Extension state: TN Effective date: 20210113 Extension state: MA Effective date: 20210113 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: EXAMINATION IS IN PROGRESS |
|
17Q | First examination report despatched |
Effective date: 20220216 |
|
GRAP | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOSNIGR1 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: GRANT OF PATENT IS INTENDED |
|
INTG | Intention to grant announced |
Effective date: 20230321 |
|
GRAJ | Information related to disapproval of communication of intention to grant by the applicant or resumption of examination proceedings by the epo deleted |
Free format text: ORIGINAL CODE: EPIDOSDIGR1 |
|
GRAL | Information related to payment of fee for publishing/printing deleted |
Free format text: ORIGINAL CODE: EPIDOSDIGR3 |
|
GRAS | Grant fee paid |
Free format text: ORIGINAL CODE: EPIDOSNIGR3 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: EXAMINATION IS IN PROGRESS |
|
GRAP | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOSNIGR1 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: GRANT OF PATENT IS INTENDED |
|
P01 | Opt-out of the competence of the unified patent court (upc) registered |
Effective date: 20230523 |
|
INTC | Intention to grant announced (deleted) | ||
INTG | Intention to grant announced |
Effective date: 20230616 |
|
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: THE PATENT HAS BEEN GRANTED |
|
AK | Designated contracting states |
Kind code of ref document: B1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: FG4D |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: EP |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R096 Ref document number: 602019036196 Country of ref document: DE |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: FG4D |
|
REG | Reference to a national code |
Ref country code: SE Ref legal event code: TRGR |
|
REG | Reference to a national code |
Ref country code: LT Ref legal event code: MG9D |
|
REG | Reference to a national code |
Ref country code: NL Ref legal event code: MP Effective date: 20230830 |
|
REG | Reference to a national code |
Ref country code: NO Ref legal event code: T2 Effective date: 20230830 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: GR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20231201 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IS Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20231230 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: RS Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20230830 Ref country code: LV Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20230830 Ref country code: LT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20230830 Ref country code: IS Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20231230 Ref country code: HR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20230830 Ref country code: GR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20231201 Ref country code: FI Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20230830 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: NL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20230830 |
|
REG | Reference to a national code |
Ref country code: ES Ref legal event code: FG2A Ref document number: 2834057 Country of ref document: ES Kind code of ref document: T3 Effective date: 20240326 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: SM Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20230830 Ref country code: RO Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20230830 Ref country code: EE Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20230830 Ref country code: DK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20230830 Ref country code: SK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20230830 Ref country code: PT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20240102 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R097 Ref document number: 602019036196 Country of ref document: DE |
|
PLBE | No opposition filed within time limit |
Free format text: ORIGINAL CODE: 0009261 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: CZ Payment date: 20240624 Year of fee payment: 6 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: SI Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20230830 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: PL Payment date: 20240621 Year of fee payment: 6 |
|
26N | No opposition filed |
Effective date: 20240603 |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: UEP Ref document number: 1605526 Country of ref document: AT Kind code of ref document: T Effective date: 20230830 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: TR Payment date: 20240624 Year of fee payment: 6 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: GB Payment date: 20240725 Year of fee payment: 6 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FR Payment date: 20240730 Year of fee payment: 6 |