CN104160058A - Steel for producing parts for railway, railway crossings and switches and method for producing said parts - Google Patents
Steel for producing parts for railway, railway crossings and switches and method for producing said parts Download PDFInfo
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- CN104160058A CN104160058A CN201380012280.1A CN201380012280A CN104160058A CN 104160058 A CN104160058 A CN 104160058A CN 201380012280 A CN201380012280 A CN 201380012280A CN 104160058 A CN104160058 A CN 104160058A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
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- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- E—FIXED CONSTRUCTIONS
- E01—CONSTRUCTION OF ROADS, RAILWAYS, OR BRIDGES
- E01B—PERMANENT WAY; PERMANENT-WAY TOOLS; MACHINES FOR MAKING RAILWAYS OF ALL KINDS
- E01B5/00—Rails; Guard rails; Distance-keeping means for them
- E01B5/02—Rails
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- E—FIXED CONSTRUCTIONS
- E01—CONSTRUCTION OF ROADS, RAILWAYS, OR BRIDGES
- E01B—PERMANENT WAY; PERMANENT-WAY TOOLS; MACHINES FOR MAKING RAILWAYS OF ALL KINDS
- E01B7/00—Switches; Crossings
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- E—FIXED CONSTRUCTIONS
- E01—CONSTRUCTION OF ROADS, RAILWAYS, OR BRIDGES
- E01B—PERMANENT WAY; PERMANENT-WAY TOOLS; MACHINES FOR MAKING RAILWAYS OF ALL KINDS
- E01B7/00—Switches; Crossings
- E01B7/10—Frogs
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- E—FIXED CONSTRUCTIONS
- E01—CONSTRUCTION OF ROADS, RAILWAYS, OR BRIDGES
- E01B—PERMANENT WAY; PERMANENT-WAY TOOLS; MACHINES FOR MAKING RAILWAYS OF ALL KINDS
- E01B7/00—Switches; Crossings
- E01B7/28—Crossings
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Organic Chemistry (AREA)
- Metallurgy (AREA)
- Civil Engineering (AREA)
- Structural Engineering (AREA)
- Architecture (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Forging (AREA)
Abstract
This invention relates to a wrought steel for producing parts for railway, railway crossings or railway switches comprising (in weight percent): -0.01 - 0.15 % carbon; -at most 0.5 % silicon; -10 - 15 % manganese; -at least 0.6 to 3.95 % molybdenum; -optionally one or more of the following elements i.0.05 to 0.2 % nickel and/or ii.0.05 to 0.2 % cobalt and/or iii.0.02 to 0.30 % Cr and/or iv.0.05 to 0.2 % copper; v. at most 5 ppm H; vi. at most 0.20 % V; vii. at most 0.10 % Nb; viii. at most 0.20 % Ti and/or Zr; ix. at most 50 ppm B; x. at most 250 ppm N; xi. at most 0.2 % Al; xii. at most 0.08 % S; xiii. at most 0.08 % P; xiv. at most 1.5 % W; -and balance iron and inevitable impurities and to a method of producing the wrought steel and its use.
Description
The present invention relates to for the production of the forged steel of the part of track crossing and switch and relate to the method for the production of described part.
Switch and crossing (S & C) are the parts of rail system, and in track circuit, in use they stand sizable load.
Several technology are just being used to produce these S & C.At present, significantly the S & C part of ratio is manufactured with cast austenitic manganese steel (AMS).Due to its high work hardening capacity impacting, excellent in toughness after solution treatment and water quenching and under work hardening condition extraordinary wear resistance, thereby conventionally use AMS.The C that the nominal chemical composition analysis of AMS is 1.2%, 13% Mn and 0.5% Si, the body hardness that its generation scope is 200-250HB.After a certain amount of transportation, the hardness of described S & C can reach the level of 500-550HB.
AMS also has many shortcomings, for example 0.2% low yielding stress.Rail switch (point) and crossing, in the common serious shock load condition of experience of viability, cause viscous deformation and work hardening, this by the strength of materials rise to further plastic flow more have resistivity level.Yet inevitably relative dimensions variation is unwanted under original unhardened condition.In road, the load of difference causes inhomogeneous sclerosis and local viscous deformation in-orbit, and the poor riding quality of gained finally need to be rebuild by weld deposit the profile of distortion.As a result, the AMS in heavy thrust load application needs grinding frequently to remove deformation (lipping) and to need repair by welding to repair Deformation Height loss.
AMS is the material that is difficult to be cast or machined into the needed complicated shape of S & C.And, any change of the track of track crossing is needed to new casting mould, make the production of uncommon crossing profile very expensive.The freezing range that AMS is narrow causes many holes type defect, and it can be the cracking starting point of in use seeing.Conventionally, the hole in AMS crossing occurs in approximately 10 degree of depth to 15mm from new surface, once and reach this degree of depth, due to the risk of the hole initiation crackle by any remnants, REPAIR WELDING just becomes unrealistic to rebuild described crossing.For AMS parts, within 10 years, be conventionally regarded as ordinary life, because surpass the repair by welding so serious to such an extent as to that continue to remedy that become of the degree of this time limit defect, be uneconomic, and must replace described parts.Further problem about AMS is the thermolability of austenitic microstructure, and this causes material to be difficult to welding.Difficulty in this welding is not only problems during parts described in repair by welding in position, and is also problem in the process of parts manufacture, because rail must be welded on described assembly before in being arranged on track circuit.
As the result of these problems, several surrogates for the conventional AMS intersection shape of the mouth as one speaks have been developed.Some S & C consist of the material of composition metal interlayer form, wherein contact the part of wheel of the train passing through difference forms by having, steel plate hard, wear-resisting of microstructure and character makes.The bottom of these article is manufactured by basic steel compositions.These solutions provide conventionally has the more cheap surrogate that good welding can toolability, but the character of crossing protuberance (nose) depends on the precision level of the steel compositions that forms described crossing protuberance.In many cases, such composition does not mate with wearing and tearing and the rolling contact fatigue resistivity particularly being provided by AMS crossing.And these solutions are difficult to due to the composite intermediate layer of different steel produce.
Another surrogate of AMS is to provide the high manganese part with work hardening layer before part is installed in the line.Pre-hardening technology in surface can comprise shot-peening, roll-in or explosion hardening.In these technology, explosion hardening is normally preferably selected, because it provides enough thick in to meet the hardened layer of the service requirements of described S & C.
Yet, by these surface hardening technology, be difficult to control the thickness of hardened layer.And surface hardening does not solve welding can toolability problem and the casting flaw relevant to the high manganese part of casting.
Therefore, the inventor sets about design for the solution of these problems.
The object of this invention is to provide conduct to AMS and the particularly Novel forging steel for S & C to the surrogate of casting AMS.
Another object is to provide as the Novel forging steel for S & C to the surrogate of AMS, and described forged steel is for can easily welding by the crown (top-of-head) REPAIR WELDING step in-situ repair.
Another object be to provide to protuberance impact (batter) by more have resistivity Novel forging steel.
Another object is to provide the Novel forging steel for S & C, and described forged steel is welding for conventional perlite rail.
Another object is to provide the Novel forging steel for S & C, and described forged steel can resistance flash butt welding for conventional perlite rail.
By being provided for producing the forged steel of the part of track, track crossing or track switch, reach one or more object of the present invention, described forged steel comprises (by weight percentage):
The carbon of 0.01-0.15%;
0.5% silicon at the most;
The manganese of 10-15%;
The molybdenum of 0.6-3.95% at least;
Choose any one kind of them or multiple lower column element:
I.0.05-0.2% nickel and/or
The cobalt of ii.0.05-0.2% and/or
The Cr of iii.0.02-0.30% and/or
The copper of iv.0.05-0.2%;
V. the H of 5ppm at the most;
Vi. 0.20% V at the most;
Vii. 0.10% Nb at the most;
Viii. 0.20% Ti and/or Zr at the most;
Ix. the B of 50ppm at the most;
X. the N of 250ppm at the most;
Xi. 0.2% Al at the most;
Xii. 0.08% S at the most;
Xiii. 0.08% P at the most;
Xiv. 1.5% W at the most;
With surplus be iron and inevitable impurity.
The present invention allows to produce the former material base of single type, described former material base can be machined to subsequently to any crossing design that need to meet local condition.Computer-controlled machining causes tolerance more accurate under reducing costs.The crossing that has many different angles due to track, to meet local demand, is therefore also reflected in the various casting mould cause of needs AMS castings production these and this in their relatively high costs.Therefore, the invention provides significant cost.
The effect of carbon in this steel is in order mainly to obtain the enough hardness of steel by solution strengthening.On the other hand, high-carbon content causes the increase of the amount of residual austenite, causes the reduction of hardness.Owing to all forming carbon network in manufacturing conditions and after welding, the increase of carbon content will enlarge markedly the risk of embrittlement of grain boundaries in these steel.Therefore, in order to keep the delicate balance between hardness and embrittlement risk, for these steel carbon contents need to for 0.01%-0.15%, (all compositions provide with weight percent, except as otherwise noted).More preferably carbon content is 0.01-0.12%.As the result of their lower carbon contents, most these alloys can easily weld.In order further to improve weldability, carbon content is preferably at the most 0.10, and more preferably at the most 0.08.
In order to realize required microstructure, carbon content is at least 0.01% and preferably at least 0.02%.From the suitable minimum carbon content of angle of steel-making, be 0.04%.
Manganese is that austenite promotes element.Its stable austenite, increases the temperature range that austenite exists.
Change is presented at according to the manganese content in steel of the present invention under at least 10% manganese content and obtains highest hardness.Under 15% very high manganese level for example, lower hardness is to insufficient level.It is deciding factor for life-span of most of track parts (comprising S & C) that hardness and wear resistance has strong dependency and wear resistance.Low wear rate means the repairing that does not need so continually part.Have lower than the steel of 10% manganese content from higher than 10% those between different owing to microstructure of the significant difference of wear resistance.Manganese level lower than 10% causes complete martensitic microstructure, yet shows residual austenite, ε-martensite (close-packed hexagonal or hcp martensite) and martensitic mixing microstructure higher than 10% level.Preferably, manganese level is at least 11%.The wear resistance of steel of having found to have complete martensitic microstructure is poorer than those of the mixing microstructure that contains martensite and retained austenite.Yet, increase manganese content and also cause the increase of residual austenite.Under the manganese content higher than 15%, the level of residual austenite becomes the increase hardness of enough height to such an extent as to martensitic phase more than the hardness of being offset by softer austenitic increase ratio, and overall hardness and the wear resistance of steel declines described in result.The resistivity of On Crack Propagation is high and relevant with degradation failure very slowly.For this reason, exist any fatigue cracking for development before complete failure occurs to be found and to remove or repair boosting chances of affected one or more parts from use.Based on above-mentioned demonstration, manganese content is preferably at least 11 and at the most 15%.Because manganese is also expensive alloy element, find that suitable maximum manganese content is 14% or even 13%.Find that suitable minimum manganese content is 11.5%.When being 12-13%Mn, described manganese content obtains the maximum value of hardness and wear resistance.Under these levels, one side residual austenite+ε-martensite and the on the other hand martensitic amount of hard are about 50:50, and the gratifying combination of impelling strength and hardness is provided thus.
Molybdenum is being effective aspect increase impelling strength.In addition,, due to the scavenging(action) of molybdenum for phosphorus, prevented temper embrittlement phenomenon.Under the level of Mo 0.6%, the increase aspect impelling strength merits attention, but obtains further and increase under the value higher than 0.6%.In the trend stable (off) under 1.5% value that is increased in aspect impelling strength.Therefore, it need to be 0.6%-3.95% that molybdenum in this steel adds, and preferably molybdenum content is at the most 2.95% and/or at least 1.25%.Find that 1.5% molybdenum content is the suitable minimum value for stable notched bar impact strength.From angle in conjunction with cost and technology, find that 1.90% molybdenum content is suitable maximum value, because cause only moderate further improvement higher than the interpolation of 1.90% value.
Find that silicon has minimum impact to the impelling strength of these steel and wear resistance, although it provides the increase in tensile strength and hardness via solution strengthening really.In steel manufacture process, it also serves as reductor.On this basis, the maximum value of the Si of recommendation 0.5%.Find that suitable minimum content is 0.10 or even 0.15%, and/or find that suitable maximum value is 0.40 or even 0.35%.
Nickel (Ni), cobalt (Co) and copper (Cu) promote the mode of element to have and the similar effect of manganese by them as austenite.Can add to a certain extent these elements and replace manganese, or except manganese, also add these elements.Can be with the maximum value of every kind of element 1.0%, add up at the most 3% to add Ni, Co and Cu.Preferably the maximum value of Ni, Co and/or Cu is 0.5%.
According to alloy of the present invention, having proved can be easily mach.One or more that if necessary, can carry out that sulphur, calcium, tellurium or selenium or any other known machinable strengthen element add to promote (further) these alloys.
Phosphorus content remains on conventionally lower than 0.08%, preferably lower than 0.05% and preferably lower than 0.02%, so that the trend of hot tearing minimizes.Phosphorus is the residual element in these steel.If do not add sulphur to strengthen machinable, sulphur content remains on the impurity level lower than 0.02% conventionally so.If interpolation sulphur, so suitable maximum is 0.08%, is preferably 0.05%.If add lower column element as alloy element, so preferred scope is as follows: the V of 0.02-0.20%, the Ti of the Nb of 0.02-0.10%, 0.02-0.20% are, the B of the Zr of 0.02-0.20%, 5-50ppm and the N of 10-250ppm.Suitable maximum level is 0.10% V, 0.075% Nb, 0.10% Zr and/or 0.10% Ti.B, V, Nb, Zr and Ti contribute to the grain refining of steel.
Steel according to the present invention is preferably silicon deoxidation.The degree of cleaning of supposing described steel keep meeting according to the standard aspect the maximum value being mingled with at aluminum oxide, described steel can also be aluminium deoxidation or the deoxidation of aluminium-silicon.When adding as alloy element, maximum total aluminium content is 0.2%.Preferably total aluminium content (when adding as alloy element) is 0.02-0.15%.Metallicity aluminium content (as oxide compound exist) will be lower, this depend on when interpolation aluminium described in the oxide content of steel melt.
Steel according to the present invention has lower than 5ppm, preferably lower than 3.5ppm and more preferably less than the hydrogen richness of 2.5ppm.
Although chromium preferably remains on the impurity level lower than 0.15%, chromium is not to have a mind to add, and for some application, can add the chromium of the level that is up to 0.3%.The highest suitable chromium content is 0.2%.
It should be noted that, can also be for the production of foundry goods according to steel compositions of the present invention, but because low carbon composition is more expensive than normal AMS Clarence Hadfield (Hadfiled) types of steel with high-carbon content, and under its casting condition, do not produce than AMS better properties, thereby use composition according to the present invention produce cast material be economically do not have attractive.
According to second aspect, invention be also embodied in for the production of track rail road, for example, for the method for the forged steel part of track crossing or track switch, said method comprising the steps of:
Provide the parent material having according to the composition of any one in claim 1 to 10, for example piece or ingot;
At suitable temperature, provide parent material, for being rolled into plate or rail, wherein
I. this hot-rolled sheet has the thickness being enough to by hot-rolled sheet machining part, or
Ii. wherein this rail has required rail profile, for
A. be machined to the part for track crossing and switch, for example visible blade (switchblade) or
B. as rail;
Make this plate or rail cooling to realize required mechanical properties after last thermal distortion;
By hot rolling cooling plate or trailer, process the part for track crossing and track switch;
Can be by be used forged steel to produce as crossing or for the part of crossing by hot rolling cooling plate machining forged steel.Can also provide forged steel to there is the rail form of required geometric profile, and can these hot rollings cooling rail are welded on part or for being machined to visible blade.This rail also can former state be used.
The method according to this invention allows to produce the base with different lengths, this base can be machined to the crossing with wide angular range subsequently.Hot-rolled sheet can also be cut into thinner length, be machined to subsequently visible blade.Yet, in order to form visible blade, can preferably ingot bar (cast bloom) be rolled into and there is the rail of required geometric profile and this rail of after this machining to manufacture visible blade.
According to the third aspect, invention be also embodied in produced according to the invention and/or there is the purposes in track, track crossing or track switch according to the forged steel part of composition of the present invention, preferably wherein by original position repair by welding step REPAIR WELDING steel part at least in part.
According to the resistance flash butt welding of steel of the present invention preferably by first using the stainless steel inset that is soldered to crossing is carried out before it being welded to perlite rail, stainless steel inset as Sandwich filling thing to improve the consistency for the complete weld seam of height.
Steel according to the present invention can be used for producing the part for track crossing and switch, for example the railway frog in universal cross mouth as shown in Figure 1.This shows the monoblock cast(ing) railway frog in universal cross mouth.This self-shield railway frog of track of not protecting has the flange improving on railway frog, at wheel, loads on the face of wheel during by railway frog.Although be mainly intended to, forged steel according to the present invention is applied in to the part (for example railway frog and visible blade) for track, track crossing or track switch, but find that this steel is also suitable for other rail parts, for example expansion pipe, insulation rail joint or rail.
Railway frog also forms a part for track switch, and also for level connection joint point (flat crossing).Designing this railway frog " does not fall into " in described breach to guarantee wheel to pass the breach in rail; Wheel and rail profile guarantee that wheel is always supported by least one rail.In order to ensure wheel, along suitable flangeway, guard rail or protection track are arranged in the rail relative with railway frog.Fig. 2 shows at dexter railway frog and the guard rail on limit leftward.Conventionally, railway frog or double frog will be standby by steel according to the present invention.
Now by non-limiting example below, the present invention is described in further detail.
Produce a series of foundry goods and in table 1, provided chemical constitution.
Table 1-is according to the chemical constitution of steel of the present invention.
| ? | C | Si | Mn | Mo | P | S | Al | N | Cr | Ni | Cu | V | Nb | W | Ti | Co |
| 10JF17 | 0.08 | 0.25 | 12.60 | 1.53 | 0.008 | 0.007 | 0.002 | 0.008 | ＜0.005 | ＜0.005 | ＜0.005 | 0.002 | 0.001 | 0.001 | 0.0001 | 0.001 |
| 10JF18 | 0.047 | 0.25 | 12.47 | 2.51 | 0.008 | 0.006 | 0.002 | 0.007 | ＜0.005 | ＜0.005 | ＜0.005 | 0.001 | 0.001 | 0.001 | 0.0001 | 0.001 |
| 10JF15 | 0.055 | 0.37 | 12.87 | 2.06 | 0.011 | 0.011 | 0.002 | 0.008 | 0.07 | 0.03 | 0.02 | 0.002 | 0.001 | 0.01 | 0.0001 | 0.001 |
| 10JF16 | 0.053 | 0.35 | 12.82 | 2.34 | 0.011 | 0.009 | 0.002 | 0.013 | 0.07 | 0.03 | 0.02 | 0.002 | 0.001 | 0.01 | 0.0001 | 0.001 |
| 10FJ41-Cr | 0.064 | 0.24 | 12.48 | 1.68 | 0.006 | 0.005 | 0.005 | 0.0110 | 0.15 | 0.050 | 0.020 | 0.010 | 0.007 | 0.001 | 0.0012 | 0.004 |
| 10FJ41-Mo?Cr | 0.06 | 0.26 | 12.33 | 1.51 | 0.010 | 0.008 | 0.002 | 0.0081 | 0.020 | 0.020 | 0.020 | 0.001 | 0.007 | 0.001 | 0.0012 | 0.004 |
| 12JF26 | 0.046 | 0.24 | 12.85 | 1.55 | 0.008 | 0.0045 | 0.006 | ＜0.001 | 0.09 | 0.03 | 0.03 | 0.087 | 0.005 | 0.01 | 0.0018 | 0.001 |
| 12JF27 | 0.048 | 0.23 | 12.89 | 1.55 | 0.008 | 0.005 | 0.005 | ＜0.001 | 0.09 | 0.03 | 0.03 | ＜0.001 | 0.042 | 0.01 | 0.0016 | ＜0.001 |
| The horizontal * of maximum contaminant | ? | ? | ? | ? | 0.02 | 0.02 | 0.005 | ＜0.012 | 0.15 | 0.1 | 0.05 | 0.03 | 0.01 | 0.01 | 0.01 | 0.01 |
* Sn, maximum contaminant level=0.01% of As
The mechanical property of described steel is outstanding, as shown in Table 2.
Table 2-mechanical properties
* A (50) can not be determined exactly, but is at least 12%.* wearing test not yet completes, but PRELIMINARY RESULTS shows the value of the slip of 3-5mg/m.
According to the rolling contact fatigue of steel of the present invention (RCF) resistivity the double plate wear testing of assessment by room temperature carry out, follow 900MPa rolling contact stress, 5% slip level and whole test duration apply a small amount of lubricant.At Fletcher & Beynon, " Development of a machine for closely controlled rolling contact fatigue and wear testing ", J.Test.Eval.28 (2000), has described this test and for the device of these tests in 267-275.Described RCF resistivity is defined as to the cycle number starting for crackle.Test data shows that novel material is than 2 times of current alternative rail steels in market.In the situation that senior to heat treated rail, for example, the cycle number before crackle starts is generally 110000 circulations.And, the comparable RCF resistivity of RCF resistivity of described novel material demonstration and AMS and maraging steel (being respectively AMS and MS in Fig. 3), and RCF crackle only starts from after 300000 circulations.Aspect low cycle fatigue, find that steel according to the present invention is surpassing AMS aspect this.
With relatively showing of other rail material steel according to the present invention good notched bar impact strength is shown, described value surpasses to be enough in order to produce the value for the object of the part of track crossing and switch.Fig. 4 illustrates as the Sha Erpi of the function of molybdenum content (Charpy) toughness value (at 20 ℃ in J), and minimum value of this proof Mo is 0.6%.Open circulation is corresponding to microalloying sample 12JF26 and 27.
Described material has very high work hardening rate, the stress increase (seeing Fig. 5 a and 5b) after cause in the low cycle fatigue test process of about 400MPa in standard NF12 test sample+three circulations of 1 to-1%.At the amplifier section of Fig. 5 a shown in Fig. 5 b, wherein the stress increase in first (1 *), second (2 *) and the 3rd (3 *) inferior working cycle is clearly visible.
For according to the assessment of the rolling contact wear resistance of steel of the present invention also the double plate wear testing by room temperature carry out, but follow the rolling contact pressure of 750MPa, after 2130 circulations, measuring wear rate (sees Fig. 6, wherein the contact wear resistance of rolling is plotted as to the function of Brinell hardness HB.Illustration shows the amplifier section of curve).Find that the wear rate (take mg/m slip) of material according to the invention (black circles in Fig. 6) is as low-down, in the scope of the slip in 0-5mg/m, and with AMS with develop recently
there is the identical order of magnitude (rhombus in Fig. 6 represents).
Due to its low carbon content, according to the weldability of steel of the present invention, be good, and more much better than the weldability of AMS, making for weldability is wherein the application of problem, for example, in production and the use of the part for track crossing and switch, described new steel is preferred selection.
Claims (15)
1. for the production of the forged steel of the part of track, track crossing or track switch, it comprises (by weight percentage):
The carbon of 0.01-0.15%;
0.5% silicon at the most;
The manganese of 10-15%;
The molybdenum of 0.6-3.95% at least;
Choose any one kind of them or multiple lower column element:
I.0.05-0.2% nickel and/or
The cobalt of ii.0.05-0.2% and/or
The Cr of iii.0.02-0.30% and/or
The copper of iv.0.05-0.2%;
V. the H of 5ppm at the most;
Vi. 0.20% V at the most;
Vii. 0.10% Nb at the most;
Viii. 0.20% Ti and/or Zr at the most;
Ix. the B of 50ppm at the most;
X. the N of 250ppm at the most;
Xi. 0.2% Al at the most;
Xii. 0.08% S at the most;
Xiii. 0.08% P at the most;
Xiv. 1.5% W at the most;
With surplus be iron and inevitable impurity.
2. according to the steel of claim 1, it comprises at the most 0.12% C and/or at least 11% Mn, and/or 2.95% Mo at the most.
3. according to the steel of claim 1, it comprises at the most 0.02% S and 0.02% P at the most.
4. according to the steel of any one in claims 1 to 3, it comprises 0.10% C at the most.
5. according to the steel of any one in claim 1 to 4, it comprises 14% Mn at the most.
6. according to the steel of any one in claim 1 to 5, it comprises at least 0.10% Si.
7. according to the steel of any one in claim 1 to 6, the retained austenite that comprises at least 15 volume % at its hot-rolled state and/or the retained austenite that comprises at least 15 volume % in the process as the part of track, track crossing or track switch at it.
8. according to the steel of any one in claim 1 to 7, it comprises:
At least 1% Mo, preferably at least 1.25% and/or
2.45% Mo at the most, preferably at the most 1.90%.
9. according to the steel of any one in claim 1 to 8, it comprises at least 0.02% C.
10. according to the steel of any one in claim 1 to 9, wherein said ladle is containing 0.05 to 0.1% vanadium and/or 0.025 to 0.075% Nb.
The method of the 11. forged steel parts for the production of track, track crossing or track switch, it comprises the following steps:
Provide the parent material having according to the composition of any one in claim 1 to 10, for example piece or ingot;
At suitable temperature, provide parent material, for being rolled into plate or rail, wherein
I. this hot-rolled sheet has the thickness being enough to by hot-rolled sheet machining part, or
Ii. wherein this rail has the rail profile needing, for
A. be machined to the part for track crossing and switch, for example visible blade or
B. as rail;
Iii. make described plate or rail cooling to realize required mechanical properties after last thermal distortion;
By hot rolling cooling plate or trailer, process the part for track crossing or track switch;
12. according to the production method of the steel of the forged steel part for the production of track, track crossing or track switch of claim 11, and it comprises one or more rails are welded to the additional step on this part.
13. according to the method for claim 11 or 12, and wherein the forged steel part for track, track crossing or track switch is railway frog or double frog or visible blade.
14. is that produce according to claim 11 to any one in 13 and/or have a purposes in track, track crossing or track switch according to the forged steel part of the composition of any one in claim 1 to 10.
15. according to the purposes of the forged steel part of claim 15, wherein by original position repair by welding step forged steel part described in REPAIR WELDING at least in part.
Applications Claiming Priority (7)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| EP12152514 | 2012-01-25 | ||
| EP12152514.1 | 2012-01-25 | ||
| US201261595014P | 2012-02-03 | 2012-02-03 | |
| EP12153948.0 | 2012-02-03 | ||
| US61/595,014 | 2012-02-03 | ||
| EP12153948 | 2012-02-03 | ||
| PCT/EP2013/051517 WO2013110798A1 (en) | 2012-01-25 | 2013-01-25 | Steel for producing parts for railway, railway crossings and switches and method for producing said parts |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN104160058A true CN104160058A (en) | 2014-11-19 |
Family
ID=48872901
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201380012280.1A Pending CN104160058A (en) | 2012-01-25 | 2013-01-25 | Steel for producing parts for railway, railway crossings and switches and method for producing said parts |
Country Status (11)
| Country | Link |
|---|---|
| US (1) | US20150028165A1 (en) |
| EP (1) | EP2807283A1 (en) |
| JP (1) | JP2015510548A (en) |
| KR (1) | KR20140119153A (en) |
| CN (1) | CN104160058A (en) |
| AU (1) | AU2013213544A1 (en) |
| BR (1) | BR112014018242A2 (en) |
| HK (1) | HK1203572A1 (en) |
| MX (1) | MX2014008972A (en) |
| RU (1) | RU2014134530A (en) |
| WO (1) | WO2013110798A1 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113668299A (en) * | 2021-08-20 | 2021-11-19 | 宜兴市鑫煜科技有限公司 | Integrally-cast frog structure for railroad tramcar turnout and preparation process thereof |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR101543898B1 (en) * | 2013-12-24 | 2015-08-11 | 주식회사 포스코 | Steel having excellent impact toughness of welding zone and welding property |
| CA3071616A1 (en) | 2017-08-01 | 2019-02-07 | The Chamberlain Group, Inc. | System for facilitating access to a secured area |
| US11055942B2 (en) | 2017-08-01 | 2021-07-06 | The Chamberlain Group, Inc. | System and method for facilitating access to a secured area |
| JP6801747B2 (en) * | 2018-06-28 | 2020-12-16 | Ｊｆｅスチール株式会社 | Manufacturing method for austenitic rails |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS60128242A (en) * | 1983-12-15 | 1985-07-09 | Nippon Steel Corp | High manganese steel for nonmagnetic drill collar |
| JPH0313525A (en) * | 1989-06-10 | 1991-01-22 | Kobe Steel Ltd | Production of high-mn nonmagnetic steel having excellent sr brittle resistant characteristic, high strength and high toughness |
| CN1745963A (en) * | 2005-10-17 | 2006-03-15 | 大连交通大学 | Forging (rolling) manufacture of high-manganese steel frog centering rail |
| CN101074469A (en) * | 2007-06-12 | 2007-11-21 | 燕山大学 | Forged (rolled) abrasive austenic permanganic steel and its manufacture |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE1178880B (en) * | 1961-10-21 | 1964-10-01 | Huettenwerk Oberhausen Ag | Process for the production of steel, wear-resistant, naturally hard single-material rails |
| FR2407987A1 (en) * | 1977-11-03 | 1979-06-01 | Creusot Loire | AUSTENITIC STEEL WITH MOLDABLE AND WELDABLE MANGANESE |
| DE19735285C2 (en) * | 1997-08-14 | 2001-08-23 | Butzbacher Weichenbau Gmbh | Process for the production of a track part |
| CN1061385C (en) * | 1998-06-19 | 2001-01-31 | 四川工业学院 | High-performance abrasion-resistant steel for switch tongue of high-speed or quasi high-speed railway |
| GB0204558D0 (en) * | 2002-02-27 | 2002-04-10 | Allen Edgar Eng | Railway crossings, etc |
-
2013
- 2013-01-25 BR BR112014018242A patent/BR112014018242A2/en not_active IP Right Cessation
- 2013-01-25 EP EP13702617.5A patent/EP2807283A1/en not_active Withdrawn
- 2013-01-25 US US14/373,741 patent/US20150028165A1/en not_active Abandoned
- 2013-01-25 AU AU2013213544A patent/AU2013213544A1/en not_active Abandoned
- 2013-01-25 JP JP2014553744A patent/JP2015510548A/en active Pending
- 2013-01-25 MX MX2014008972A patent/MX2014008972A/en unknown
- 2013-01-25 WO PCT/EP2013/051517 patent/WO2013110798A1/en active Application Filing
- 2013-01-25 CN CN201380012280.1A patent/CN104160058A/en active Pending
- 2013-01-25 KR KR1020147023571A patent/KR20140119153A/en not_active Application Discontinuation
- 2013-01-25 RU RU2014134530A patent/RU2014134530A/en not_active Application Discontinuation
-
2015
- 2015-04-22 HK HK15103913.1A patent/HK1203572A1/en unknown
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS60128242A (en) * | 1983-12-15 | 1985-07-09 | Nippon Steel Corp | High manganese steel for nonmagnetic drill collar |
| JPH0313525A (en) * | 1989-06-10 | 1991-01-22 | Kobe Steel Ltd | Production of high-mn nonmagnetic steel having excellent sr brittle resistant characteristic, high strength and high toughness |
| CN1745963A (en) * | 2005-10-17 | 2006-03-15 | 大连交通大学 | Forging (rolling) manufacture of high-manganese steel frog centering rail |
| CN101074469A (en) * | 2007-06-12 | 2007-11-21 | 燕山大学 | Forged (rolled) abrasive austenic permanganic steel and its manufacture |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113668299A (en) * | 2021-08-20 | 2021-11-19 | 宜兴市鑫煜科技有限公司 | Integrally-cast frog structure for railroad tramcar turnout and preparation process thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2015510548A (en) | 2015-04-09 |
| BR112014018242A2 (en) | 2017-07-04 |
| EP2807283A1 (en) | 2014-12-03 |
| MX2014008972A (en) | 2015-03-19 |
| WO2013110798A1 (en) | 2013-08-01 |
| AU2013213544A1 (en) | 2014-08-28 |
| RU2014134530A (en) | 2016-03-20 |
| HK1203572A1 (en) | 2015-10-30 |
| KR20140119153A (en) | 2014-10-08 |
| US20150028165A1 (en) | 2015-01-29 |
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