奥地利专利AT512792A4 Process for the production of bainitic rail steels

专利PDF首页>>奥地利专利

专利附录

专利说明

权利要求

类似技术

同族专利

引用文献

法律状态

优先权

专利摘要:
In a rail part, particularly a rail for low alloy steel rail vehicles, the steel in the rail head of the rail part has a ferrite content of 5-15 vol% and a multiphase bainite structure consisting of upper and lower bainite parts.
公开号:AT512792A4
申请号:T990/2012
申请日:2012-09-11
公开日:2013-11-15
发明作者:Peter Pointner；Norbert Frank
申请人:Voestalpine Schienen Gmbh；
IPC主号:

专利说明:

The invention relates to a rail part, in particular a rail for rail vehicles made of a low-alloy steel.
The invention further relates to a method for producing a rail part from a hot-rolled profile and to a device for carrying out this method.
Recently, the weight of transported loads in rail traffic and the traveling speed have been steadily increased to increase the efficiency of rail transportation. Rail tracks are therefore subject to difficult operating conditions and must therefore have a higher quality to withstand the higher loads. Concrete problems are manifested in a sharp increase in wear, particularly in the rails mounted in bends, and in the occurrence of fatigue failure, which primarily develops on the running edge, which is the main contact point of the rail with the wheels in the bow. This leads to rolling contact fatigue damage (RCF). Examples of RCF surface damage are e.g. Head checks (rolling fatigue), spalling (flaking), squats (plastic surface deformations), slip waves and scratches. These damage to the surface results in shortened rail life, increased noise emissions and operational disabilities. The increased occurrence of errors is also accelerated by the ever-increasing traffic loads. The immediate consequence of this development is an increased need for maintenance of the rails. However, the growing need for maintenance is in conflict with the ever-shrinking maintenance windows. Higher tensile densities reduce the • · · · ♦ 2 t ·% · ♦ · · · · · t ·
• »« «
Periods in which rails can be processed, more and more.
Although the above-mentioned damage can be eliminated in the early stages by grinding, but the rail is to be replaced in case of severe damage. Therefore, attempts have been made in the past to improve both the wear resistance and the resistance to RCF damage in order to increase the life cycle of the rails. This was done i.a. through the introduction and use of bainitic rail steels.
Bainite is a microstructure that can be produced during the heat treatment of carbon steel by isothermal transformation or continuous cooling. Bainite forms at temperatures and cooling rates that are intermediate to those for perlite or martensite formation. In contrast to the formation of martensite, folding processes in the crystal lattice and diffusion processes are coupled here, as a result of which various conversion mechanisms are possible. Due to the dependence on cooling rate, carbon content, alloying elements and the resulting formation temperature, the bainite has no characteristic structure. Bainite, like perlite, consists of the phases ferrite and cementite (Fe3C), but differs from pearlite in shape, size and distribution. Basically, bainite is divided into two main structural forms, the upper bainite and the lower bainite.
From AT 407057 B a rail material is known in which a structural transformation of austenite expressly only in
Area of lower bainite is formed so that the profiled rolling a hardness of at least 350 HB, in particular 450-600 HB receives.
A bainitic matrix may also be mixed with higher alloying constituents, e.g. be achieved with a high chromium content of 2.2 to 3.0 wt .-%, as described in the publications DE 102006030815 Al and DE 102006030816 Al. However, the high proportion of alloy components leads to undesirably high costs and a complex welding technology. DE 202005009259 Ul also describes a bainitic high-strength rail part made of a high-alloy steel, in particular with high alloy contents of Mn, Si and Cr. In such a high-alloyed steel, the bainite formation can be easily obtained by cooling in still air. In low-alloyed steels, on the other hand, bainit formation is only possible if controlled cooling is carried out.
Accordingly, for example, DE 1533982 describes a method for heat treatment of rails, in which the still rolling temperature having rail is taken after leaving the rolling stand with a lifting device and immersed with the rail head down in a maintained at a constant temperature fluidized bed and cooled there, wherein a bainitic microstructure is achieved by selecting the fluid bed temperature between 380 and 460 ° C and leaving the rail in the fluidized bed for between 300 and 900 seconds depending on its temperature. λ Α · ♦ ····················································································· ♦♦ «♦♦♦ · I« ······ ······································
A further production of high-strength rails of low-alloy steels with bainitic structures for achieving a better resistance to fatigue damage due to rolling contact has become known from EP 612852 B1. The head of the rail is subjected to accelerated cooling at a rate of 1-10 ° C / sec from the austenite region to a cooling-off temperature of 500-300 ° C. After this rapid cooling, the rail head is further cooled to near room temperature using either natural cooling with heat recovery or forced cooling at a rate of 1-40 ° C / min.
Although the measures mentioned could delay, but not prevent, the formation and propagation of cracks on the rail head.
The invention therefore aims to improve a rail part, in particular a rail, which is to consist of a low-alloy steel for cost reasons and for reasons of welding, to the effect that even with increased wheel loads no Rollkontaktermüdungsschäden and in particular no cracks on the running edge and arise at the tread. Furthermore, the wear resistance should be increased so far that a service life of more than 30 years can be ensured. Finally, the track part should be well weldable and similar other material properties such as e.g. a similar electrical conductivity and a similar coefficient of thermal expansion have been proven in rail construction proven steels. Λ • · ···································································································. ···································· #
Furthermore, the invention aims to provide a simple production process, which is characterized by a short process time (avoiding incandescent phases), high reproducibility and high cost-effectiveness. The method is intended to produce long rails of e.g. be suitable over 100 m in length, over the entire rail length constant material properties are to be ensured.
To solve this problem, the invention according to a first aspect provides a rail part of the type mentioned, which is developed such that the steel in the rail head of the rail part a ferrite content of 5-15 vol .-% and a multi-phase bainite structure consisting of upper and having lower bainite portions. By combining a ferritic structure with a bainitic structure, excellent toughness properties and a sufficiently high hardness are achieved. The ferrite microstructure component serves as plasticity carrier and leads to the fact that any cracks which may have occurred can not run into the material as head checks. The ferrite content gives the entire structure a continuous network in which the bainite is embedded. In this context, a percolation threshold (" Percolation Threshold ") which must be attained to obtain this formation of contiguous clusters.
Preferably, the ferrite is an acicular ferrite. The acicular structure is distinguished from a non-acicular structure and also from a pearlitic structure by a higher tensile strength and < * < * · «· · · · · · · · ···
* · «· · * # Φ · •% · ·« · · · · · · · · · · ···
Wear resistance. The acicular ferrite has a microstructure characterized by needle-like shaped crystallites or grains, wherein the crystallites are not uniformly aligned, but are completely unoriented, which positively affects the toughness of the steel. The unoriented arrangement of the grains leads to a mutual entanglement of the individual grains, which in combination with the multiphase bainite effectively prevents cracking or propagation. In particular, this achieves the result that any cracks ("head checks") that have formed on the surface do not grow into the depth of the material, as shown, for example, in US Pat. in a pearlite structure is the case. The track part is therefore only exposed to wear, so that its duration of use can be defined precisely and further observation due to cracking need not occur.
Also crucial is the presence of a multiphase bainite comprising upper and lower bainite portions. The upper bainite is produced in the upper temperature range of bainite formation and has a needle-like structure similar to martensite. In this upper temperature range of bainite formation, favorable diffusion conditions exist, so that the carbon can diffuse to the grain boundaries of the ferrite needles. This produces irregular and interrupted cementite crystals. Because of the random distribution, the texture often has a grainy appearance, so the upper bainite is sometimes referred to as granular bainite. The lower bainite is formed during isothermal and continuous cooling in the lower temperature range of bainite formation. The austenite accumulates in carbon as a result of ferrite formation; on further cooling, the austenite areas are transformed into ferrite, cementite, etc. * * * * «« t * ♦ · · ··· «« · »· · ·« «Needley bainite and martensite. Bainitizing reduces residual stresses and increases toughness.
The mixing ratio between lower and upper bainite can basically be varied within wide limits according to the respective requirements. In particular, the choice of mixing ratio determines the hardness of the steel. It is particularly preferred in the context of the invention that the proportion of the upper bainite 5-75 vol .-%, in particular 20-60 vol .-% and the proportion of the lower bainite 15-90 vol .-%, in particular 40-85 vol .-%, is.
The ferrite content is preferably 8-13% by volume.
Precondition for a complete bainitic transformation is the carbide formation from the austenite. Because carbides absorb large amounts of carbon, they are carbon sinks that extract carbon from austenite. If carbide formation is prevented or retarded by, for example, silicon as an alloying element, larger amounts of austenite are not converted. After quenching to room temperature, they are then completely or partially present as retained austenite. The amount of retained austenite depends on how far the
Martensite start temperature has lowered in the remaining austenite. In the context of the invention, it is advantageous if the smallest possible proportions of austenite and / or martensite remain. Therefore, in this context, the invention preferably provides that the steel in the rail head of the rail part has a residual martensite / austenite content of < 2% by volume.
As already mentioned, according to the invention low-alloy steels are used in order to minimize costs and to improve weldability. In general, the low-alloyed steel in the context of the invention preferably contains silicon, manganese and chromium as alloy constituents, as well as possibly vanadium, molybdenum, phosphorus, sulfur and / or nickel.
In the context of the invention, a steel is to be referred to as low-alloyed steel if no alloy constituent is present in a proportion of greater than 1.5% by weight.
Particularly good results could be achieved with a low-alloy steel with the following directional analysis: 0.4-0.55% by weight C 0.3-0.6% by weight Si 0.9-1.4% by weight Mn 0.3-0.6 wt% Cr 0.1-0.3 wt% V 0.05-0.20 wt% Mo 0-0.02 wt% P 0-0 , 02 wt .-% S 0 - 0.15 wt.% Ni
A particularly good suitability for highly stressed sections is preferably given when the rail part in the head region has a tensile strength Rm greater than 1150 N / mm2. Furthermore, the track part in the head area preferably has a hardness greater than 340 HB. 9 9 ·· t «< * ï
According to a second aspect, the invention provides a method for producing the track part described above, wherein the track part is produced from a hot-rolled profile, wherein the rail head of the rolled profile is subjected to controlled cooling immediately after leaving the rolling stand with the rolling heat, wherein the controlled cooling in a first step is an accelerated cooling until reaching a first temperature permitting a ferrite formation, in a second step holding the first temperature to effect ferrite formation, in a third step further cooling in a multi-phase bainite formation permitting temperature range up to a second temperature and in a fourth step comprises holding the second temperature. The controlled cooling is preferably carried out, as known per se, by immersing at least the rail head in a liquid cooling medium.
The first step in this case preferably begins at a temperature of 740-850 ° C, in particular about 790 ° C and ends preferably at a temperature of 450-525 ° C. The cooling which takes place during the first step must be controlled in such a way that in the time-temperature conversion diagram one arrives in the area of ferrite and subsequent bainite formation, in particular no conversion in the pearlite stage. For this purpose, the accelerated cooling in the first step preferably takes place at a cooling rate of 2-5 ° C / sec. In order to achieve this cooling rate, the preferred procedure is that the rail part is completely immersed in the cooling medium during the first step. • * * t m m m m m • • • • • • • • • •
In the second step, the temperature of preferably 450-525 ° C is maintained and it is important for the performance property ferrite content, especially the acicular ferrite, with a volume fraction of 5-15%, in particular 8-13%, in particular about 10%, the holding the temperature is preferably achieved by holding the splice member in a position taken out of the cooling medium during the second step.
In a third step, a further controlled cooling is carried out for the required limitation of the ferrite content, so that a mixture of upper and lower bainite structure is formed (multiphase bainite). The temperature range in which bainitization occurs is preferably between 450-525 ° C and 280-350 ° C, i. that the rail head of the rail part in the bainite phase from 450-525 ° C to 280-350 ° C is cooled. This third step preferably extends over a period of 50-100 sec, in particular about 70 sec. In the bainite formation phase, it is sufficient if the rail part is preferably immersed in the cooling medium only with the rail head.
During the subsequent temperature maintenance of the rail part in the fourth step in the range of preferably 280-350 ° C, the hardness of the rail part is then finally fixed depending on the temperature position, falling below the martensite start temperature (usually about 280 ° C} is to be avoided since can form too many martensitic, brittle microstructural constituents in the temperature range.
The temperature hold during the fourth step is preferably by cyclic head dipping, i. that the track part is dipped cyclically into the cooling medium and removed from the cooling medium.
Since the temperature range of the bainite phase formation and the martensite start temperature depend on the alloying elements of the respective steel and their proportions, the value of the first temperature and the value of the second temperature must be accurately determined beforehand for each steel. The temperature of the rail is then continuously measured during the controlled cooling, wherein the cooling and holding sections are started or terminated upon reaching the respective temperature thresholds. Since the surface temperature of the rail can vary over the entire length of the rail part, but the cooling is carried out uniformly for the entire rail part, it is preferred that the temperature detected at a plurality of distributed over the length of the rail part measuring points and a temperature average is formed , which is used for the control of the controlled cooling.
In the bainite formation phase, austenite transforms to bainite as completely as possible. This occurs at temperatures below the perlite formation up to the martensite start temperature both isothermally and with continuous cooling. By slowly folding the austenite out, starting from the grain boundaries or impurities, strongly carbon-supersaturated ferrite crystals with cubic-body-centered crystal lattice are formed. The carbon precipitates within the ferrite grain due to the higher diffusion rate in the cubic space centered lattice in the form of spherical or ellipsoidal cementite crystals. Likewise, the carbon can diffuse into the austenite area and form carbides. **
In the context of the invention, during the third step and fourth step, cooling and temperature maintenance are carried out in such a way that a multiphase bainite is formed. During a first substep, a continuous cooling takes place at a lower cooling rate than in a second substep, in which the temperature is lowered abruptly until the second temperature is reached. During the first step, predominantly upper bainite is formed. After the abrupt cooling, in the fourth step a holding at the second temperature takes place, in which case lower bainite is formed. The duration of holding the second temperature during the fourth step determines the extent of lower bainite formation.
The upper bainite consists of acicular ferrite, which is arranged in packets. Between the individual ferrite needles there are more or less continuous films of carbides parallel to the needle axis. By contrast, lower bainite consists of ferrite plates within which the carbides form at an angle of 60 ° to the needle axis. During the controlled cooling by means of the liquid cooling medium, the cooling medium passes through three phases of the quenching process. In the first phase, the vapor film phase, the temperature at the surface of the rail head is so high that the cooling medium evaporates rapidly and forms a thin insulating vapor film (Leidenfrost effect). This steam film phase is u.a. very much from the heat of vaporization of the cooling medium, the surface finish of the rail part, such as e.g. Scale, or the chemical composition and design of the ψ * · MM MM MM MM MM MM MM MM · · · · • • • Φ Φ Φ Φ Φ Φ Φ Φ Φ Φ Φ Φ «« «« «« «« «« «« «« «« «« « · Φ * Φ "£ ^" φ · * ΦΦΦ φ φφ depending on the cooling pool. In the second phase, the cooking phase, the cooling medium comes into direct contact with the hot surface of the rail head and comes immediately to boiling, resulting in a high cooling rate. The third phase, the convection phase, begins when the surface temperature of the rail part has dropped to the boiling point of the cooling medium. In this area, the cooling speed is essentially influenced by the flow velocity of the cooling medium.
In the case of the controlled cooling provided according to the invention, the cooling medium is preferably in the vapor phase during the first step. Preference is further given to proceeding so that the cooling is controlled during the third step so that the cooling medium on the surface of the rail head first forms a vapor film and then boils on the surface. There is thus a transition from the vapor film phase into the cooking phase. The vapor film phase extends over the length of the above-mentioned first substep, in which predominantly upper bainite is produced. Upon reaching the boiling phase, the temperature abruptly drops to the second temperature, i. to preferably 280-350 ° C from.
The transition from the vapor phase to the cooking phase is usually relatively uncontrolled and spontaneous.
Since the rail temperature over the entire length of the rail part is subject to certain production-related temperature fluctuations, there is the problem that the transition from the vapor film phase into the cooking phase takes place in different lengths of the rail part at different times. This would lead to a non-uniform microstructure over the length of the rail part and consequently to uneven material properties. In order to standardize the time of transition from the steam film phase to the cooking phase over the entire rail length, a preferred procedure is that during the third step a film breaking gaseous printing medium, such as e.g. Nitrogen, along the entire length of the rail part is brought to the rail head to break the vapor film along the entire length of the rail part and to initiate the cooking phase.
In particular, it is possible to proceed so that the state of the cooling medium is monitored during the third step along the entire length of the rail part and the film-breaking, gaseous pressure medium is introduced to the rail head as soon as the first occurrence of the cooking phase is detected in a partial region of the rail length.
Preferably, the film-breaking, gaseous pressure medium is brought to the rail head approximately 20-100 seconds, in particular approximately 50 seconds after the beginning of the third step.
According to a further aspect of the invention, there is proposed a device for carrying out the method described above, comprising a coolant tank which can be filled with cooling medium, a lifting and lowering device for the rail part in order to dip and lift the rail part into the cooling tank Temperature measuring device for measuring the temperature of the rail part,
Pressure-medium generating agent, through which the pressure medium in ** ·· ·· ·· * · * ··· Μ ···· * · * · · · t * · ·· ··· · # ·· ····· The cooling medium is introduced, means for regulating the temperature of the cooling medium and a control device, which are supplied with the measured values of the temperature measuring device, and which cooperates with the raising and lowering means for controlling the raising and lowering operations and with the means for controlling the temperature of the cooling medium in dependence on the temperature readings and further with the pressure medium generating means.
Sensors are preferably provided for detecting cooling medium boiling on the surface of the rail head, the sensor measured values of which are fed to the control device in order to control the pressure medium generation means as a function of the sensor measured values. In particular, a plurality of sensors may be provided for detecting cooling medium cooking on the surface of the rail head, which are distributed over the length of the cooling pool.
Preferably, the sensor measured values of the plurality of sensors are fed to the control device, wherein the control device controls the pressure medium generating means as soon as at least one sensor detects boiling cooling medium on the surface of the rail head.
Advantageously, the control means is adapted to perform a controlled cooling, in a first step, an accelerated cooling until reaching a ferrite permitting first temperature, in a second step, holding the first temperature to effect ferrite formation, in a third Step further cooling in a temperature range allowing the polyphase bainite formation up to a t ftftft
• ft · ft ····························································································································································································
In particular, the controller may be configured to reduce the temperature of the rail head in the first step at a cooling rate of 2-5 ° C / sec to a first temperature of 450-525 ° C, the temperature of the rail head in the second step on the to maintain the first temperature and the temperature of the rail head during the third step, preferably over a period of 50-100 sec, in particular about 70 sec, to a second temperature of 280-350 ° C to reduce.
Preferably, the control means is adapted to drive the print medium generating means during the third step.
The invention will be explained in more detail with reference to embodiments.
A low alloy steel with the following directional analysis was hot rolled to form a rail with a rail profile: 0.49 wt% C 0.36 wt% Si 1.11 wt% Mn 0.53 wt% Cr 0.136 Weight% V 0.0085 wt% Mo 0.02 wt% P 0.02 wt% S 0.1 wt% Ni * 17 ** f ···· Μ ··
Immediately after leaving the rolling stand, the rail was subjected to controlled cooling with the rolling heat. The controlled cooling is explained below with reference to the time-temperature conversion diagram shown in FIG. 1, wherein the line designated by 1 represents the cooling curve. The cooling process starts at a temperature of 790 ° C. In a first step, the rail is immersed over its entire length and with its entire cross section in a cooling bath of water and it was set a cooling rate of 4 ° C / sec. After about 75 sec, a surface temperature of the railhead of 490 ° C was measured, reaching point 2, and the rail was removed from the cooling bath to maintain the temperature for a period of about 30 sec., Whereby the formation of acicular Ferrite was reached. Upon reaching point 3, the rail was again immersed in the cooling bath and cooled to point 4. At point 4, the initial boiling of the cooling water at the surface of the rail head was detected and compressed air was applied to the rail head to break the vapor film surrounding the rail head and initiate the cooking phase over the entire length of the rail.
The initiation of the cooking phase led to an abrupt drop in the temperature of the rail head, wherein this cooling was stopped when reaching a temperature of 315 ° C (item 5). By cyclic head diving this temperature was maintained for a certain time. The length of the hold time determines the composition of the multiphase bainite structure, as shown in the following examples. &Lt; • tmtttff * t * t · t · t 4 t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t t | ·
example 1
In a first embodiment, a low alloy steel with the following directional analysis by hot rolling was formed into a rail with a rail profile: 0.49 wt% C 0.36 wt% Si 1.11 wt% Mn 0.53 wt. % Cr 0.136 wt% V 0.0085 wt% Mo 0.02 wt% P 0.02 wt% S 0.1 wt% Ni
By the controlled cooling described above, the following microstructure was obtained in the rail head: about 10% by volume of acicular ferrite, about 74% by volume of "0" upper bainite, about 16% by volume of lower bainite, < 1% by volume martensite residual austenite.
The microstructure is shown in FIG. 2.
Due to the higher proportion of upper bainite, a lower hardness of the rail head was achieved than in the following, second embodiment. The following material properties were measured.
Hardness: 347 HB ft ft ft ft ft ft ft ft ft ft ft ft ft ft ft ft ft *········································································· * * * Ft * ft * ft * * ft * ft * *
Tensile strength: 1162 MPa 0.2% Yield strength: 977 MPa Elongation at break: 14.4%
Impact test:
Test at + 20 ° C: 110 J / cra2 test at -20 ° C: 95 J / cm2 Crack growth. da / dN:
Test at ΔΚ = 10 [MPaVm]: 8.9 [m / Gc]
Testing at ΔΚ = 13.5 [MPaVm]: 15.8 [m / Gc], where m / Gc = meter / gigacycle Wear resistance: (AMSLER test: slip 10%, normal force 1200N) Material wear: 1.72 mg / m2 Comparison R260 Material wear: 1.79 mg / m2 Fracture toughness: 39 MPaVm
Example 2
In the second embodiment, the same low alloy steel was used as in Example 1 and formed by hot rolling into a rail with a rail profile. The controlled cooling was carried out the same as in Example 1, but the temperature was kept longer in the fourth step than in Example 1. The following structure was achieved in the rail head: about 10 vol .-% acicular ferrite, about 15 vol. % upper bainite, about 75% by volume lower bainite, < 1% by volume martensite residual austenite.
The microstructure is shown in FIG. 3. ί t
• tt * ♦ * ♦ ** ·· M «* * *» * * «« ft · »» * · »·· f # ·· I * # · * · ·« 4 I t «· · 4 f φ «4 * 2o **« · · «· · ·»
The following material properties were measured. Hardness: 405 HB Tensile strength: 1387 MPa 0.2% Yield strength: 1144 MPa Elongation at break: 12.6%
Impact test:
Test at + 20 ° C: 100 J / cm2 Test at -20 ° C: 75 J / cm2 Crack growth da / dN:
Test at ΔΚ = 10 [MPaVm]: 9.5 [m / Gc]
Test at ΔΚ = 13.5 [MPVm]: 16.5 [m / Gc] Wear resistance; (AMSLER test: slip 10%, normal force 1200N) Material wear: 1.55 mg / m2 Comparison R2.60 Material wear: 1.79 mg / m2 Fracture toughness: 36 MPaVm

权利要求:
Claims (34)
[1]
7 7 · ♦ t ·! · ··· »·· ♦ *« ··· * * Φ * · 9 • · * · * ·

1. Rail part, in particular rail for rail vehicles, made of a low-alloy steel, characterized in that the steel in the rail head of the rail part has a ferrite content of 5-6. 15 vol .-% and a multi-phase bainite structure consisting of upper and lower Bainitanteilen has.
[2]
2. track part according to claim 1, characterized in that the proportion of the upper bainite 5-75 vol .-%, in particular 20-60 vol .-% and the proportion of lower bainite 15-90 vol .-%, in particular 40-85 Vol .-%, is.
[3]
3. track part according to claim 1 or 2, characterized in that the ferrite content is 8-13 vol.-S.
[4]
4. track part according to claim 1, 2 or 3, characterized in that the ferrite is an acicular ferrite.
[5]
5. rail part according to claim 4, characterized in that the multiphase bainite is incorporated in the acicular ferrite structure.
[6]
6. track part according to one of claims 1 to 5, characterized in that the steel in the rail head of the track part a residual martensite / austenite content of < 2% by volume.
[7]
7. track part according to one of claims 1 to 6, characterized in that the low-alloyed steel silicon, manganese and chromium and optionally vanadium, molybdenum, phosphorus, ································································································································································································
[8]
8. track part according to claim 7, characterized in that no alloying ingredient is present in a proportion of greater than 1.5 wt .-%.
[9]
9. track part according to one of claims 1 to 8, characterized in that a low-alloyed steel is used with the following directional analysis: 0.4 - 0.55 wt .-% C 0.3 - 0.6 wt .-% Si 0 , 9-1.4% by weight Mn 0.3-0.6% by weight Cr 0.1-0.3% by weight V 0.05-0.20% by weight Mo 0-0 , 02 wt .-% P 0 - 0.02 wt .-% S 0 - 0.15 wt.% Ni
[10]
10. track part according to one of claims 1 to 9, characterized in that the track part in the head region has a tensile strength Rm greater than 1150 N / mm2.
[11]
11. track part according to one of claims 1 to 10, characterized in that the track part in the head area has a hardness greater than 340 HB.
[12]
12. A method for producing a rail part according to one of claims 1 to 11 from a hot rolled profile, characterized in that the rail head of the rolled profile is subjected to a controlled cooling immediately after leaving the rolling mill with the rolling heat, * 9 ·· «t ♦ ♦♦ • · · · · · «· · · 9 ** *« φ

Wherein the controlled cooling in a first step, an accelerated cooling until reaching a first ferrite permitting temperature, in a second step, the holding of the first temperature to effect ferrite formation in one third step comprises further cooling in a multiphase bainite forming temperature range up to a second temperature and in a fourth step comprising maintaining the second temperature.
[13]
13. The method according to claim 12, characterized in that the first step at a temperature of 740-850ο0, in particular about 790 ° C begins.
[14]
14. The method according to claim 12 or 13, characterized in that- the first temperature is 450-525 ° C.
[15]
15. The method of claim 12, 13 or 14, characterized in that the second temperature is 280-350 ° C.
[16]
16. The method according to any one of claims 12 to 15, characterized in that the accelerated cooling in the first step takes place at a cooling rate of 2-5 ° C / sec.
[17]
17. The method according to any one of claims 12 to 16, characterized in that the third step extends over a period of 50-100 sec, in particular about 70 sec.
[18]
18. The method according to any one of claims 12 to 17, characterized in that the temperature at a plurality of distributed over the length of the track part measuring points 99 ·· t «** ♦ * ♦ · ** · * # ·« «*« « and a temperature average is formed which is used to control the controlled cooling.
[19]
19. The method according to any one of claims 12 to 18, characterized in that the controlled cooling takes place by immersing at least the rail head in a liquid cooling medium.
[20]
20. The method according to any one of claims 12 to 19, characterized in that the cooling during the third step is controlled so that the cooling medium at the surface of the rail head first forms a vapor film and then boiling on the surface.
[21]
A method according to claim 20, characterized in that during the third step a film breaking gaseous printing medium, e.g. Nitrogen, along the entire length of the rail part is brought to the rail head to break the vapor film along the entire length of the rail part and to initiate the cooking phase.
[22]
22. The method according to claim 21, characterized in that the state of the cooling medium is monitored during the third step along the entire length of the rail part and the film-breaking, gaseous pressure medium is introduced to the rail head, as soon as in a partial region of the rail length the first occurrence of the cooking phase is detected.
[23]
23. The method according to claim 21 or 22, characterized in that the film-breaking, gaseous pressure medium about 20-100 sec, in particular about 50 seconds after Γ 1 * · Μ 99 ** »·» · «99 9 * 9 * 999 «* 9 * * * * 9 9 * · 9 ν · 9 • * * * ^» «9 # 999 * 99 99 9 * • ^ * 9 9 * * * * * 9 * Start of the third step on the railhead is introduced.
[24]
24. The method according to any one of claims 12 to 23, characterized in that the track part is completely immersed in the cooling medium during the first step.
[25]
25. The method according to any one of claims 12 to 24, characterized in that the track part is held during the second step in a position taken out of the cooling medium position.
[26]
26. The method according to any one of claims 12 to 25, characterized in that the track part is immersed in the cooling medium during the third step only with the rail head.
[27]
27. The method according to any one of claims 12 to 26, characterized in that the track part is cyclically immersed in the cooling medium during the fourth step and taken out of the cooling medium.
[28]
28. A device for carrying out the method according to one of claims 12 to 27, comprising a the length of the rail part corresponding, can be filled with cooling medium cooling tank, a lifting and lowering device for the rail part to immerse the rail part in the cooling pool and lift out, a temperature measuring device for Measuring the temperature of the rail part, pressure medium generating means, by which the pressure medium is introduced into the cooling medium, means for controlling the temperature of the cooling medium and a control device, which the measured values of the temperature measuring device * ·· * * * · »* ** · * »·· * Φ · *» «t» v ··· * * · »* ** · *» ·· * Φ ·

And which cooperates with the raising and lowering mechanism for controlling the raising and lowering operations and with the means for controlling the temperature of the cooling medium depending on the temperature readings and further with the pressure medium generating means.
[29]
29. Device according to claim 28, characterized in that sensors for detecting boiling cooling medium are provided on the surface of the rail head, the sensor measured values of which are fed to the control device in order to control the pressure medium generating means as a function of the sensor measured values.
[30]
30. A device according to claim 29, characterized in that a plurality of sensors for detecting boiling cooling medium is provided on the surface of the rail head, which are distributed over the length of the cooling pool.
[31]
31. Device according to claim 28, 29 or 30, characterized in that the sensor measured values of the plurality of sensors are fed to the control device, wherein the control device controls the pressure medium generating means as soon as at least one sensor detects boiling cooling medium on the surface of the rail head.
[32]
32. Device according to one of claims 28 to 31, characterized in that the control device is designed to perform a controlled cooling, in a first step, an accelerated cooling until reaching a ferrite permitting first temperature, in a second step holding the first temperature, in order to obtain a ferrite formation, in a third step, a further cooling in a the t ** ** ** ··· * M * "·" t · · «*« 4 · · * · # * I

In the case of a multi-phase bainite formation, the temperature range is up to a second temperature and in a fourth step, the second temperature is maintained.
[33]
33. Device according to claim 32, characterized in that the control device is designed to reduce the temperature of the rail head in the first step at a cooling rate of 2-5 ° C / sec to a first temperature of 450-525 ° C, maintaining the temperature of the rail head in the second step at the first temperature and the temperature of the rail head during the third step preferably over a period of 50-100 sec, in particular about 70 sec, to a second temperature of 280-350 ° C. to reduce.
[34]
34. Device according to claim 32 or 33, characterized in that the control device is designed to control the pressure medium generating means during the third step. Vienna, September 11, 2012 Applicant by: Haffner and Keschmann Patentanwälte KG

类似技术:

公开号 | 公开日 | 专利标题

AT512792B1|2013-11-15|Process for the production of bainitic rail steels

AT409267B|2002-07-25|EXTREMELY HIGH-STRENGTH AUSTENITE-AGED STEELS WITH EXCELLENT DEPTH TEMPERATURE

Sivaprasad et al.2000|Effect of prestrain on fracture toughness of HSLA steels

DE112004001914T5|2006-10-19|Ball and roller bearings

WO2018108653A1|2018-06-21|Hot-rolled flat steel product and method for the production thereof

WO2016177763A1|2016-11-10|Flat steel product and method for the production thereof

EP2690184B1|2020-09-02|Produit plat en acier laminé à froid et son procédé de fabrication

EP2746409A1|2014-06-25|Method for the heat treatment a manganese steel product and manganese steel product with a special alloy

DE69730739T2|2005-09-22|Steel for piping with excellent resistance to external surface stress corrosion cracking

DE1458470B2|1974-05-09|Use of a heat-treated, ductile, high-strength steel alloy with a martensitic or bainitic structure for the production of components for aerospace engineering

EP2516075A2|2012-10-31|Thermomechanical treatment method

DE69629161T2|2004-04-15|METHOD FOR PRODUCING RAILS WITH HIGH WEAR RESISTANCE AND HIGH RESISTANCE TO INNER DEFECTS

DE60205744T2|2006-06-22|HIGH STRENGTH AND HIGH-DUCTILE STEEL PLATE WITH HYPERFINE CRYSTAL CORRUGATED STRUCTURE MANUFACTURED BY MOBILIZATION PROCESSING AND GLOWING OF COMMON CARBON STEEL STEEL, AND METHOD OF MANUFACTURING THEREOF

EP3535431B1|2021-06-09|Steel product with an intermediate manganese content for low temperature application and production method thereof

DE2302865B1|1974-07-25|Method for producing an uncoated high-strength rail

AT519669B1|2018-09-15|Rail part and method for producing a rail part

Macherauch et al.1986|Verformungsverhalten gehärteter Stähle

EP2840159B1|2017-05-10|Method for producing a steel component

DE60011666T2|2005-06-30|METHOD FOR PRODUCING ULTRA-FINE GRAIN STRUCTURE FOR UNITED OR LOW-ALLOYED STEELS

WO2017162450A1|2017-09-28|Method for temperature-treating a manganese steel intermediate product, and steel intermediate product which has been temperature-treated in a corresponding manner

DE2745241A1|1978-04-20|HIGH QUALITY STEELS WITH IMPROVED TOUGHNESS AND PROCESS FOR THEIR PRODUCTION

EP3017074B1|2018-10-17|Wear-resistant uncoated steel part

DE102011051682B4|2013-02-21|Method and apparatus for treating a steel product and steel product

EP3964592A1|2022-03-09|Hot-rolled steel sheet product and method for producing a hot-rolled steel sheet product

DE2602656A1|1976-08-05|Cooling rolled steel - to remove heat at the most efficient rate

同族专利:

公开号 | 公开日

AU2013315331A1|2015-04-16|

TW201410877A|2014-03-16|

CA2883523A1|2014-03-20|

RU2015113360A|2016-11-10|

UA110312C2|2015-12-10|

TWI496897B|2015-08-21|

AR091760A1|2015-02-25|

US20150218759A1|2015-08-06|

ZA201502151B|2016-01-27|

JP2015532946A|2015-11-16|

WO2014040093A1|2014-03-20|

CN104812918A|2015-07-29|

BR112015005189A2|2017-07-04|

RU2608254C2|2017-01-17|

AT512792B1|2013-11-15|

EP2895632A1|2015-07-22|

引用文献:

公开号 | 申请日 | 公开日 | 申请人 | 专利标题

EP0358362A1|1988-08-19|1990-03-14|The Algoma Steel Corporation, Limited|Method for the manufacture of alloy railway rails|

EP0612852A1|1993-02-26|1994-08-31|Nippon Steel Corporation|Process for manufacturing high-strength bainitic steel rails with excellent rolling-contact fatique resistance|

EP2365103A1|2008-10-31|2011-09-14|Usui Kokusai Sangyo Kaisha Limited|High-strength steel machined product and method for manufacturing the same, and method for manufacturing diesel engine fuel injection pipe and common rail|CN110904311A|2019-12-06|2020-03-24|马鞍山钢铁股份有限公司|Anti-out-of-roundness wheel steel, wheel and preparation method of wheel|FR90024E|1965-04-28|1967-09-29|Lorraine Escaut Sa|Method and installation of heat treatment of rails|

GB9313060D0|1993-06-24|1993-08-11|British Steel Plc|Rails|

US5759299A|1994-05-10|1998-06-02|Nkk Corporation|Rail having excellent resistance to rolling fatigue damage and rail having excellent toughness and wear resistance and method of manufacturing the same|

GB2297094B|1995-01-20|1998-09-23|British Steel Plc|Improvements in and relating to Carbide-Free Bainitic Steels|

CN1083013C|1996-09-29|2002-04-17|攀枝花钢铁公司|Heat treating method and apparatus for producing high duty rails by waste heat from rolling process|

AT407057B|1996-12-19|2000-12-27|Voest Alpine Schienen Gmbh|PROFILED ROLLING MATERIAL AND METHOD FOR THE PRODUCTION THEREOF|

GC0000233A|2000-08-07|2006-03-29|Exxonmobil Upstream Res Co|Weld metals with superior low temperature toughness for joining high strength, low alloy steels|

AT410549B|2001-09-13|2003-05-26|Voest Alpine Schienen Gmbh & C|DEVICE FOR TURNING ROLLED GOODS WITH LONG LENGTH|

EP1736555B1|2004-04-07|2014-12-24|Oriental Engineering Co., Ltd.|Metal part cooling method, metal part producing method, and metal part cooling device|

CZ14602U1|2004-06-22|2004-08-16|Dtávýhybkárnaáaámostárnaáa@Ás|Steel for castings of railway and streetcar points frogs|

DE102006030816A1|2006-06-30|2008-01-03|Deutsche Bahn Ag|Method for producing a high-strength frog tip and frog tip|

DE102006030815A1|2006-06-30|2008-01-03|Deutsche Bahn Ag|Method for producing high-strength tongue devices, tongue rails and / or stock rails as well as tongue device, tongue rail and / or stock rail as well as rail extensions and insulating joints|

WO2008042982A2|2006-10-03|2008-04-10|Cola Jr Gary M|Microtreatment of iron-based alloy, apparatus and method therefor, and articles resulting therefrom|

EP2089556B1|2006-10-06|2019-05-01|JFE Steel Corporation|Low yield ratio dual phase steel linepipe with superior strain aging resistance|

JP5365112B2|2008-09-10|2013-12-11|Ｊｆｅスチール株式会社|High strength steel plate and manufacturing method thereof|

JP5883211B2|2010-01-29|2016-03-09|株式会社神戸製鋼所|High-strength cold-rolled steel sheet with excellent workability and method for producing the same|CN107326302B|2017-05-26|2018-10-19|北京交通大学|A kind of anti-corrosion bainitic steel, rail and preparation method|

AT519669B1|2017-06-07|2018-09-15|Voestalpine Schienen Gmbh|Rail part and method for producing a rail part|

WO2019102258A1|2017-11-27|2019-05-31|Arcelormittal|Method for manufacturing a rail and corresponding rail|

CN110102581B|2019-04-03|2020-10-30|池州海琳服装有限公司|Cold-rolled wire steel pile detection method based on Internet of things|

CN110714377B|2019-12-10|2021-08-13|安徽浦进轨道装备有限公司|Easily-assembled support structure for magnetic suspension vehicle track|

CN112159940A|2020-10-27|2021-01-01|攀钢集团攀枝花钢铁研究院有限公司|Switch steel rail with large supercooling degree and deep hardened layer and preparation method thereof|

CN112962029B|2021-02-01|2021-12-21|广东鑫发精密金属科技有限公司|Low-hardness and easy-to-process stainless steel material for zipper buttons and preparation method thereof|

法律状态:
2018-05-15| MM01| Lapse because of not paying annual fees|Effective date: 20170911 |

优先权:

申请号 | 申请日 | 专利标题

ATA990/2012A|AT512792B1|2012-09-11|2012-09-11|Process for the production of bainitic rail steels|ATA990/2012A| AT512792B1|2012-09-11|2012-09-11|Process for the production of bainitic rail steels|

AU2013315331A| AU2013315331A1|2012-09-11|2013-06-27|Method for producing bainitic rail steels, track element and installation for carrying out the method|

TW102122931A| TWI496897B|2012-09-11|2013-06-27|Method for producing bainitic rail steel|

PCT/AT2013/000107| WO2014040093A1|2012-09-11|2013-06-27|Method for producing bainitic rail steels, track element and installation for carrying out the method|

JP2015530236A| JP2015532946A|2012-09-11|2013-06-27|Method for producing bainite-based rail steel, track element, and apparatus for carrying out this method|

BR112015005189A| BR112015005189A2|2012-09-11|2013-06-27|method for the production of bainitic steel for rail, track element and installation for carrying out the method|

UAA201503380A| UA110312C2|2012-09-11|2013-06-27|Method of manufacturing bainite rail steel, rolling track pitch and device for implementation of it|

US14/427,525| US20150218759A1|2012-09-11|2013-06-27|Method for producing bainitic rail steels, track element and installation for carrying out the method|

CN201380047032.0A| CN104812918A|2012-09-11|2013-06-27|Method for producing bainitic rail steels, track element and installation for carrying out the method|

RU2015113360A| RU2608254C2|2012-09-11|2013-06-27|Method for obtaining bainitic rail steels|

CA2883523A| CA2883523A1|2012-09-11|2013-06-27|Method for producing bainitic rail steels, track element and installation for carrying out the method|

EP13739927.5A| EP2895632A1|2012-09-11|2013-06-27|Method for producing bainitic rail steels, track element and installation for carrying out the method|

ARP130102503| AR091760A1|2012-09-11|2013-07-12|PART OF VIA, PROCEDURE TO PRODUCE SUCH PART OF VIA AND DEVICE TO CARRY OUT THAT PROCEDURE|

ZA2015/02151A| ZA201502151B|2012-09-11|2015-03-27|Method for producing bainitic rail steels ,track element and installation for carrying out the method|

[返回顶部]