CN106086663B - A kind of hypereutectoid rail and preparation method thereof - Google Patents

A kind of hypereutectoid rail and preparation method thereof Download PDF

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Publication number
CN106086663B
CN106086663B CN201610552631.3A CN201610552631A CN106086663B CN 106086663 B CN106086663 B CN 106086663B CN 201610552631 A CN201610552631 A CN 201610552631A CN 106086663 B CN106086663 B CN 106086663B
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weight
rail
steel billet
temperature
hypereutectoid
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CN106086663A (en
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韩振宇
邹明
郭华
陶功明
汪渊
王春建
贾济海
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Pangang Group Panzhihua Iron and Steel Research Institute Co Ltd
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Pangang Group Panzhihua Iron and Steel Research Institute Co Ltd
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Priority to BR112019000331-2A priority patent/BR112019000331A2/en
Priority to US16/317,416 priority patent/US20190226040A1/en
Priority to AU2017295527A priority patent/AU2017295527B2/en
Priority to PCT/CN2017/085651 priority patent/WO2018010494A1/en
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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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • 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
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • 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
    • 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
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C21D2211/001—Austenite
    • 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

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

Abstract

The present invention relates to railway territory, discloses a kind of hypereutectoid rail and preparation method thereof, and this method includes being rolled on the steel billet containing V and Ti, wherein, on the basis of the gross weight of steel billet, the steel billet contains 0.85 0.94 weight % carbon, start rolling temperature TOpenWith finishing temperature TEventuallyMeet below equation with the relation of content of vanadium [V] and Ti content [Ti]：TOpen=1100+a ([V]+5 [Ti]), TEventually=750+b ([V]+5 [Ti]), wherein, 500≤a≤800,300≤b≤500；On the basis of the gross weight of steel billet, [V] is 0.03 0.08 weight %, and [Ti] is 0.011 0.02 weight %, and [V]+5 [Ti] is 0.12 0.14 weight %.Hypereutectoid rail prepared by this method has excellent tough combination property.

Description

A kind of hypereutectoid rail and preparation method thereof
Technical field
The present invention relates to railway territory, in particular it relates to a kind of hypereutectoid rail and preparation method thereof.
Background technology
Pearlite steel rail is the product that railway territory dosage is maximum, use range is most wide.With railway axle weight and drive a vehicle close Degree is continuously increased, after the normal carbon rail and microalloying rail of existing hypereutectoid carbon content are even across heat treatment, most High intensity is only 1300-1400MPa, and between wheel track under multidirectional complicated heavy load effect, rail head position easily forms too fast abrasion, core Hurt, the service lifes of rail such as wound, stripping chip off-falling are greatly reduced and jeopardize traffic safety.Therefore, in the traffic condition of harshness In the case of irreversible, the toughness and tenacity of rail is improved, and then the service life for extending rail just seems particularly significant.For For heavy haul railway sharp radius curve section, abrasion progressively turn into the primary factor for influenceing the life-span.Research confirms, improves abrasion Performance most effective way is to improve the hardness of rail.Under the conditions of existing pearlite steel rail, it is most effective, most cheap to improve hardness Mode is to improve the carbon content in steel.However, the raising of carbon content reduces the toughness plasticity index for causing rail, and it is existing tough The lower limit that plasticity has been on active service safely close to rail, increase rail is issued in equal service condition if the index further reduces The risk of raw brittle failure.Using heat treatment technics, strong refined crystalline strengthening effect is relied on, can be carried while rail strong hardness is improved The toughness plasticity of high rail, in practice it has proved that, heat-treated rail generally possesses higher compared with identical component hot rolled rail tough comprehensive Energy.Even so, if carbon content further improves, such as more than 0.85% is reached, even if heat treatment technics is to toughness plasticity Lifting amplitude is also limited, it is necessary to meet rail toughness and tenacity under the conditions of hypereutectoid carbon content by the application of new technology Need.
The content of the invention
The purpose of the present invention be overcome hypereutectoid rail in the prior art tough combination property it is bad the problem of, there is provided one Kind hypereutectoid rail, and the preparation method of the hypereutectoid rail.
The present inventor has found that, for high-carbon content rail, fining austenite grains are simultaneously final in research process Refinement pearlite piece interlamellar spacing not only contributes to intensity, and the raising to toughness plasticity index also has notable benefit；Although refinement is difficult to understand Family name's body crystal grain finally the lifting effect to toughness plasticity far away from refined crystalline strengthening effect, but for the higher hypereutectoid steel of carbon content Rail, under conditions of toughness plasticity has tended to the limit, if further fining austenite grains, then keep high intensity simultaneously to rail It is significant to obtain higher toughness plasticity.Refinement for austenite crystal, CN102803536A《Ductility is excellent Pearlitic high-carbon rail and its manufacture method》In describe following method：1. carrying out low temperature reheating after steel rail rolling, but deposit The problem of be inside austenite crystal melt remain thick carbide, make on the contrary acceleration cool down after pearlitic structrure it is tough Plasticity reduces.Meanwhile reheat and the economy problems such as manufacturing cost is high, production efficiency is low also be present；2. precipitate pinning Ovshinsky Body crystal boundary, fining austenite grains, so as to improve the obdurability of final rail；Research shows, for the steel of hypereutectoid carbon content Rail, influence of the austenitic state to final products performance is limited.However, when carbon content is more than 0.85%, austenite shape Influence of the state to the performance of product can not be ignored.
The present inventor also found in research process, to reach fining austenite grains and finally obtaining performance Excellent rail product, start rolling temperature, finishing temperature need to be carried out being uniformly coordinated control, could finally prepare hypereutectoid condition Under tough high comprehensive performance rail, if in combination with the control of chemical composition and cooling technique to steel billet, can make It is standby go out the more excellent rail of performance.
Thus, the present invention provides a kind of method for preparing hypereutectoid rail, wherein, this method includes to contain V's and Ti Steel billet is rolled, wherein, on the basis of the gross weight of steel billet, the steel billet contains 0.85-0.94 weight % carbon, open rolling temperature Spend TOpenWith finishing temperature TEventuallyMeet below equation with the relation of content of vanadium [V] and Ti content [Ti]：
TOpen=1100+a ([V]+5 [Ti]),
TEventually=750+b ([V]+5 [Ti]),
Wherein, 500≤a≤800,300≤b≤500；
On the basis of the gross weight of steel billet, [V] is 0.03-0.08 weight %, and [Ti] is 0.011-0.02 weight %, and [V]+5 [Ti] is 0.12-0.14 weight %.
Present invention also offers the hypereutectoid rail that the above method is prepared.
Using the method for the invention prepare hypereutectoid rail have excellent tough combination property (such as toughness plasticity and Contact resistance fatigue behaviour), it can particularly obtain the hypereutectoid steel that microstructure is pearlite+micro secondary cementite Rail.
Other features and advantages of the present invention will be described in detail in subsequent specific embodiment part.
Brief description of the drawings
Accompanying drawing is for providing a further understanding of the present invention, and a part for constitution instruction, with following tool Body embodiment is used to explain the present invention together, but is not construed as limiting the invention.In the accompanying drawings：
Fig. 1 is the micro-organization chart for the hypereutectoid rail that the embodiment of the present invention 1 obtains.
Embodiment
The embodiment of the present invention is described in detail below.It is it should be appreciated that described herein specific Embodiment is merely to illustrate and explain the present invention, and is not intended to limit the invention.
The end points of disclosed scope and any value are not limited to the accurate scope or value herein, these scopes or Value should be understood to comprising the value close to these scopes or value.For number range, between the endpoint value of each scope, respectively It can be combined with each other between the endpoint value of individual scope and single point value, and individually between point value and obtain one or more New number range, these number ranges should be considered as specific open herein.
The invention provides a kind of method for preparing hypereutectoid rail, wherein, this method is included the steel billet containing V and Ti Rolled, wherein, on the basis of the gross weight of steel billet, the steel billet contains 0.85-0.94 weight % carbon, start rolling temperature TOpen With finishing temperature TEventuallyMeet below equation with the relation of content of vanadium [V] and Ti content [Ti]：
TOpen=1100+a ([V]+5 [Ti]),
TEventually=750+b ([V]+5 [Ti]),
Wherein, 500≤a≤800,300≤b≤500；
On the basis of the gross weight of steel billet, [V] is 0.03-0.08 weight %, and [Ti] is 0.011-0.02 weight %, and [V]+5 [Ti] is 0.12-0.14 weight %.
C is that pearlite steel rail improves strong hardness, promotes most important, the most cheap element of perlitic transformation, when C content is small When 0.85%, even if using accelerating to cool down after rolling, high intensity needed for heavy haul railway and corresponding wear-resistant can not be also obtained Performance；When C content is more than 0.94%, the secondary cementite being distributed along crystal boundary will be separated out at original austenite crystal prevention, is deteriorated The impact flexibility of rail, rail contact resistance fatigue behaviour are greatly reduced.Therefore, C content is limited to 0.85%-0.94%.
When V is under room temperature condition, the solubility in steel is very low, and is such as present in austenite grain boundary in the hot rolling Or other regions, in the form of the vanadium carbonitride of micronized particles shape separate out, or with the compound precipitations of Ti in steel, suppress austenite crystal The growth of grain, high performance purpose is put forward so as to reach crystal grain thinning；When [V] is less than 0.03 weight %, Carbonitride Precipitation containing V It is limited, it is difficult to play and strengthen effect；When [V] is more than 0.08 weight %, thick carbonitride is easily formed, deteriorates the tough of rail Plasticity.Therefore, [V] is 0.03-0.08 weight %.
Austenite crystal when main functions of the Ti in steel is refinement heating, rolling and cooling, finally increases rail Elongation percentage and rigidity, it is one of important addition element of the present invention.When [Ti] is less than 0.011 weight %, formed in rail Carbide quantity be extremely limited；When [Ti] is more than 0.02 weight %, on the one hand because Ti is strong carbonitride-forming elements, Caused TiC is on the high side will to make rail excessive high hardness, and another aspect TiC is on the high side to be enriched with segregation to form thick carbide, is not only dropped Low toughness plasticity, also rail contact surface under impact loading is caused to be easy to ftracture and cause to be broken.Therefore, [Ti] is 0.011- 0.02 weight %.
V, Ti with the affinity such as C, N and forms the quantity of carbide and form and has significant difference in steel, but forms carbon The effect of nitride fining austenite grains is similar.By taking V as an example, in the relatively low steel of N content, ferrite matrix is solid-solution in For V content more than 50%, and in the higher steel of N content, the V being solid-solution in steel is more than 20%, and residue 70% is with vanadium carbonitride Form separate out.In the present invention, individually improvement of the addition V or Ti to performance be not notable, while such as adding 0.09% V The rail strength for not adding Ti still is able to reach 1350MPa, but elongation percentage is generally below 10%, and individually adds Ti microalloyings, The intensity of rail is unable to reach 1350MPa requirements, therefore, contains V and Ti, also, [V]+5 in steel billet of the present invention simultaneously [Ti] is 0.12-0.14 weight %.
In the case of preferable, [V] is 0.045-0.055 weight %, and [Ti] is 0.014-0.02 weight %, and [V]+5 [Ti] is 0.12-0.13 weight %.
According to the present invention, the steel billet of above-mentioned composition can be obtained by the conventional method of this area, for example with converter or Molten steel of the electric furnace smelting containing mentioned component, through al-free deoxidation, external refining, Fruit storage, continuous casting is 250mm × 250mm- Cooling enters in heating furnace and heated after 450mm × 450mm section steel billets, and billet heating temperature is more than 1200 DEG C, is incubated to not surpassing Crossing 3h ensures to come out of the stove after steel billet section blank temperature is uniform, removes iron scale, can obtain steel billet of the present invention, specifically Process will not be repeated here.
According to the present invention, during billet rolling is rail, with start rolling temperature and the difference of finishing temperature, with reference to Different [V] and [Ti], the size of precipitated phase, distribution and varying topography are obvious, and then there is also bright in the rail property of acquisition Significant difference is different, studies and finds through the present inventor, as start rolling temperature TOpenWith finishing temperature TEventuallyMeet with the relation of [V]+5 [Ti] During above formula, it can be ensured that tiny in steel, Dispersed precipitate vanadium carbonitride and titanium carbon nitride fully dissolve and separated out, so that The hypereutectoid rail prepared has excellent toughness plasticity and contact resistance fatigue behaviour.In order to ensure precipitated phase is to toughness plasticity and resistance to The contribution of fatigue behaviour maximizes, under preferable case, in above formula, and 780≤a≤800,470≤b≤500.
According to the present invention, on the basis of the gross weight of steel billet, the steel billet can also contain Si：0.4-0.9 weight %, Mn：0.7-1.3 weight %, Cr：0.2-0.6 weight %, P≤0.02 weight %, S≤0.008 weight %, N：0.06-0.09 weights Amount ‰.
According to the present invention, Si is present in ferrite and austenite as the solution strengthening element in steel improves the strong of tissue Degree.The present invention preferably controls Si content the toughness plasticity that in above range, with Intensive intervention effect, can strengthen rail, optimization The lateral performance of rail, be advantageous to improve the safety in utilization of rail.
According to the present invention, Mn can form solid solution with the Fe in steel billet, improve the intensity of ferrite and austenite.Together When, Mn is carbide former again, into cementite after can partly substitute Fe atoms, increase the hardness of carbide, it is final to increase Add the hardness of steel.The present invention preferably controls Mn content in above range, can be kept away while ensuring compared with high strengthening effect Exempt to influence toughness plasticity because of carbide excessive high hardness in steel.
According to the present invention, Cr can form continuous solid solution with the Fe in steel billet, and be in steel with C-shaped into a variety of carbide One of main intensified element.In addition, Cr can uniformly in steel carbide distribution, improve the polishing machinees of steel.The present invention is excellent Choosing controls Cr content the toughness plasticity in above range, being advantageous to improve rail.
, according to the invention it is preferred to by N content control in above range, be advantageous to improve the tough comprehensive of rail under room temperature condition Close performance.
In the case of further preferably, on the basis of the gross weight of steel billet, the steel billet contains Si：0.55-0.65 weights Measure %, Mn：1.25-1.3 weight %, Cr：0.4-0.55 weight %, P≤0.014 weight %, S≤0.005 weight %, N： 0.06-0.07 weight ‰.
A preferred embodiment of the invention, methods described can also include：After rolling, when rail head top layer Temperature TTop layerIt is reduced to than finishing temperature TEventuallyAt low 20-50 DEG C, rail head is quickly cooled down；When the process quickly cooled down So that rail head skin temperature TTop layerFor 450-550 DEG C when, stopping quickly cooling down and continue to be air-cooled to room temperature.
According to the present invention, rail head skin temperature T during quick cooling beginning is controlledTop layerRail head table when stopping with quick cooling Layer temperature within the above range, can prevent that the secondary cementite being distributed along crystal boundary may be formed in rail, be advantageous to improve The toughness plasticity of rail.
According to the present invention, to the cooling velocity quickly cooled down, there is no particular limitation, can be that this area is conventional Selection.But separated out to reduce secondary cementite, improve the intensity index and abrasion resistance properties of rail, under preferable case, institute It is 2-5 DEG C/s to state the cooling velocity quickly cooled down, preferably 4.5-4.9 DEG C/s.
According to the present invention, to the embodiment quickly cooled down, there is no particular limitation, can be the routine of this area Selection, such as the embodiment quickly cooled down can apply cooling in the rail head top surface of the rail and two sides to be situated between Matter.
According to the present invention, there is no particular limitation for the selection to the cooling medium, can be the conventional selection of this area, As long as present invention cooling purpose can be reached.Under preferable case, the cooling medium is that compressed air and/or water smoke mix Liquid.
Present invention also offers the hypereutectoid rail being prepared by the above method.It should be appreciated that the present invention provides Hypereutectoid rail have with above-mentioned steel billet composition composition.Hypereutectoid rail of the present invention has excellent toughness plasticity With contact resistance fatigue behaviour.
The present invention will be described in detail by way of examples below.In following examples, " room temperature " refers to " 25 DEG C ".
The chemical composition that steel billet contains used by following examples and comparative example is as shown in table 1, wherein, except table 1 In element beyond, surplus is Fe and inevitable impurity：
Table 1
Embodiment 1-6
According to the rolling shown in the reference numeral of table 2 with quick cooling technique by the 1# in table 1 to 6# billet rollings into 60kg/ M rail, and quickly cooled down with compressed air, the rail that above-mentioned completion is handled then is air-cooled to room temperature, obtained common Analyse rail A1 to A6.
Table 2
Comparative example 1-6
According to the rolling shown in the reference numeral of table 3 with quick cooling technique by the 1# in table 1 to 6# billet rollings into 60kg/ M rail, and quickly cooled down with compressed air, the rail that above-mentioned completion is handled then is air-cooled to room temperature, obtained common Analyse rail D1 to D6.
Table 3
Test case 1
Hypereutectoid rail A1-A11 and D1-D6 prepared by embodiment 1-11 and comparative example 1-6 is carried out according to following methods Performance detection, specifically：
By GB/T228.1-2010《Metal material tensile testing at ambient temperature》The tensile property of hypereutectoid rail is determined, is surveyed Obtain Rm(tensile strength), A% (elongation), as a result as shown in table 4；
The U-shaped impact property of rail head normal temperature of hypereutectoid rail is determined by the conventional method of this area, as a result as shown in table 4；
By GB/T 13298-1991《The metal microstructure method of inspection》Using MeF3 light microscope determining hypereutectoid steels The microscopic structure of rail, measures that microscopic structure result is as shown in table 4, and A1 microscopic structure is as shown in Figure 1.
Table 4
Note：P+Fe3CⅡ(micro-) refers to pearlite+micro secondary cementite；P+Fe3CⅡ(few) refers to pearlite+a small amount of secondary Cementite；" micro " and " a small amount of " is relative relation, and " micro " is less relative to the amount of " a small amount of " expression, mainly for showing Secondary cementite in embodiment in hypereutectoid rail microscopic structure is than less in comparative example.
It can be seen that from embodiment 1-6 and comparative example 1-6 results contrast, microscopic structure assay shows, all rail Tissue is pearlite+secondary cementite (Fe3CⅡ), unlike, it is brilliant using present component and corresponding process conditions lower edge The secondary cementite quantity that boundary separates out is less, is more beneficial for improving the toughness plasticity and service safety of rail.Come from performance indications See, in the case of similar in embodiment and comparative example rail tensile strength, the rate elongation and rail of hypereutectoid rail of the present invention The head U-shaped impact property of normal temperature greatly improves, and is more beneficial for improving the contact resistance fatigue behaviour of rail.
The preferred embodiment of the present invention described in detail above, still, the present invention are not limited in above-mentioned embodiment Detail, in the range of the technology design of the present invention, a variety of simple variants can be carried out to technical scheme, this A little simple variants belong to protection scope of the present invention.
It is further to note that each particular technique feature described in above-mentioned embodiment, in not lance In the case of shield, can be combined by any suitable means, in order to avoid unnecessary repetition, the present invention to it is various can The combination of energy no longer separately illustrates.
In addition, various embodiments of the present invention can be combined randomly, as long as it is without prejudice to originally The thought of invention, it should equally be considered as content disclosed in this invention.

Claims (10)

  1. A kind of 1. method for preparing hypereutectoid rail, it is characterised in that this method includes being rolled on the steel billet containing V and Ti System, wherein, on the basis of the gross weight of steel billet, the steel billet contains 0.85-0.94 weight % carbon, start rolling temperature TOpenAnd finish to gauge Temperature TEventuallyMeet below equation with the relation of content of vanadium [V] and Ti content [Ti]：
    TOpen=1100+a ([V]+5 [Ti]),
    TEventually=750+b ([V]+5 [Ti]),
    Wherein, 500≤a≤800,300≤b≤500；
    On the basis of the gross weight of steel billet, [V] is 0.03-0.08 weight %, and [Ti] is 0.011-0.02 weight %, and [V]+5 [Ti] is 0.12-0.14 weight %.
  2. 2. according to the method for claim 1, wherein, [V] is 0.045-0.055 weight %, [Ti] is 0.014-0.02 weights % is measured, and [V]+5 [Ti] is 0.12-0.13 weight %.
  3. 3. method according to claim 1 or 2, wherein, on the basis of the gross weight of steel billet, the steel billet also contains Si： 0.4-0.9 weight %, Mn：0.7-1.3 weight %, Cr：The weight % of 0.2-0.6 weight %, P≤0.02 weight %, S≤0.008, N：0.06-0.09 weight ‰.
  4. 4. according to the method for claim 3, wherein, on the basis of the gross weight of steel billet, the steel billet contains Si：0.55- 0.65 weight %, Mn：1.25-1.3 weight %, Cr：The weight % of 0.4-0.55 weight %, P≤0.014 weight %, S≤0.005, N：0.06-0.07 weight ‰.
  5. 5. method according to claim 1 or 2, wherein, methods described also includes：After rolling, when rail head top layer temperature Spend TTop layerIt is reduced to than finishing temperature TEventuallyAt low 20-50 DEG C, rail head is quickly cooled down；When the process quickly cooled down makes Obtain rail head skin temperature TTop layerFor 450-550 DEG C when, stopping quickly cooling down and continue to be air-cooled to room temperature.
  6. 6. according to the method for claim 5, wherein, the cooling velocity quickly cooled down is 2-5 DEG C/s.
  7. 7. according to the method for claim 6, wherein, the cooling velocity quickly cooled down is 4.5-4.9 DEG C/s.
  8. 8. according to the method for claim 5, wherein, the embodiment quickly cooled down is on the rail head top of the rail Face and two sides apply cooling medium.
  9. 9. according to the method for claim 8, wherein, the cooling medium is compressed air and/or water smoke mixed liquor.
  10. 10. the hypereutectoid rail being prepared as the method described in any one in claim 1-9.
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BR112019000331-2A BR112019000331A2 (en) 2016-07-14 2017-05-24 hyperutectoid rail and method of production
US16/317,416 US20190226040A1 (en) 2016-07-14 2017-05-24 Hypereutectoid rail and manufacturing method thereof
AU2017295527A AU2017295527B2 (en) 2016-07-14 2017-05-24 A hypereutectoid rail and manufacturing method thereof
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CN106086663B (en) * 2016-07-14 2018-03-06 攀钢集团攀枝花钢铁研究院有限公司 A kind of hypereutectoid rail and preparation method thereof
CN107739806B (en) * 2017-10-10 2019-10-11 攀钢集团研究院有限公司 High toughness plasticity hypereutectoid steel rail and its manufacturing method
CN107675084B (en) * 2017-10-10 2019-05-10 攀钢集团研究院有限公司 High-carbon high-strength tenacity pearlite steel rail and its manufacturing method
CN107739983A (en) * 2017-10-30 2018-02-27 攀钢集团攀枝花钢铁研究院有限公司 A kind of hypereutectoid rail and its production method
CN107747040A (en) * 2017-10-31 2018-03-02 攀钢集团攀枝花钢铁研究院有限公司 Corrosion-resistant rail in high speed railway preparation method
CN107779768A (en) * 2017-10-31 2018-03-09 攀钢集团攀枝花钢铁研究院有限公司 Method for producing corrosion-resistant rail for high-speed railway
CN112718855A (en) * 2020-11-30 2021-04-30 攀钢集团攀枝花钢铁研究院有限公司 Hypereutectoid steel rail and preparation method thereof
CN115094338B (en) * 2022-07-27 2023-09-22 内蒙古科技大学 Hypereutectoid steel for steel rail and preparation method thereof

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