CN107675082B - Traumatic resistance rail and its manufacturing method - Google Patents
Traumatic resistance rail and its manufacturing method Download PDFInfo
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- CN107675082B CN107675082B CN201710934078.4A CN201710934078A CN107675082B CN 107675082 B CN107675082 B CN 107675082B CN 201710934078 A CN201710934078 A CN 201710934078A CN 107675082 B CN107675082 B CN 107675082B
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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
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/04—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rails
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- 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)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Articles (AREA)
Abstract
The invention belongs to rail manufacturing technology fields, and in particular to a kind of traumatic resistance rail and its manufacturing method.Uneven for prior art preparation pearlite steel rail rail head cross-section performance, the bad problem of obtained pearlite steel rail performance, the present invention provides a kind of manufacturing methods of traumatic resistance rail, comprising the following steps: a, by hot rolling of steel billet at rail；B, when rail surface central temperature is air-cooled to 800~850 DEG C, it is blown cooling medium to rail head top surface, rail head two sides and rail head two sides lower jaw, being cooled to end face center temperature is 540~570 DEG C；C, stop to rail head two sides lower jaw be blown, continue to rail head top surface, rail head two sides blowing cooling medium, be cooled to rail head skin temperature be 460~500 DEG C after, be air-cooled to room temperature.The superior rail of performance is prepared in such a way that control composition of steel, two sections of acceleration are cooling in the present invention, is suitable for the prominent section application of fatigue defect.
Description
Technical field
The present invention relates to a kind of rail, more particularly, are related to a kind of traumatic resistance rail and its manufacturing method.
Background technique
The fast development of railway proposes requirements at the higher level to rail military service performance.It is continuous complete with China express railway net
Kind, existing passenger-cargo mixed fortune trunk line will gradually implement heavy loading transformation, and large conveying quantity, high axle load, high density are the following heavily loaded iron
The developing direction on road.Critical component of the rail as railway, the superiority and inferiority of quality, performance height and railway conevying efficiency with
Traffic safety is closely bound up.With the promotion of railway transport capacity, rail Service Environment is further harsh, complicated, and all kinds of hurts are prominent
Out, part sharp radius curve section rail occur too fast abrasion simultaneously, removing hurts, the service life such as chip off-falling can not be with main track
Rail matching, constrains the further development of railway transportation.
Currently, to improve the performance of curve section rail, it is main to use pearlite steel rail online or the side of heat-treated offline
Method makes the fast quickly cooling in rail head position by way of the rail head position blowing pressurized air or water mist gaseous mixture to austenitizing rail
But, to obtain the lamellar pearlite tissue refined in rail head surface layer to certain depth, crystal grain refinement is relied on to realize the same of obdurability
Step improves, so that achieving the purpose that wear-resistant, contacting fatigue resistance is synchronous improves.It is fresh both at home and abroad in terms of acceleration cooling procedure
There is cooling nozzles arrangement mode to report the research that rail property influences.
Patent CN101646795B " wear resistance and the damaging excellent pearlite steel rail of high internal hardness type of endurance and
Its manufacturing method " in define the manufacturing method of pearlite steel rail of high internal hardness type a kind of, which is characterized in that by steel hot rolling
At rail shape, make 850~950 DEG C of finishing temperature, then, with 1.2~5 DEG C/sec of cooling velocity, by the table of rail's end portion
Temperature of the layer more than pearlitic transformation start temperature is quickly cooled to 400~650 DEG C.The patent only defines heat-treatment of rail
Different phase cools down starting and final temperature and corresponding cooling rate range, is not directed to the specific type of cooling.
Patent CN105483347A discloses " a kind of heat treatment process of pearlite steel rail hardening ", it is characterized in that: by steel
Rail is heated to 880~920 DEG C, keeps the temperature 10~15min, according to steel grade difference, is as cold as specific temperature with specific cooling rate range
Section keeps the temperature 30s, then air-cooled, specifically: material is the pearlite steel rail hardening process system of U75V are as follows: 880~920 DEG C of heat preservations
10~15min is cooled to 570~600 DEG C with 8~15 DEG C/s cooling rate, then air-cooled to 20~25 with the cooling rate of 0.2~0.5 DEG C/s
℃；Material is the pearlite steel rail hardening process system of U76CrRE are as follows: 850~900 DEG C keep the temperature 10~15 minutes, with 6~10
DEG C/s cooling rate is cooled to 590~610 DEG C, then it is air-cooled to 20~25 DEG C with the cooling rate of 0.2~0.5 DEG C/s.The board of the patent disclosure
Number specific refrigerating mode is equally not directed to for the heat treatment process of two kinds of materials of U75V, U76CrRE.
Patent CN103898303A discloses " a kind of heat treatment method and turnout rail of turnout rail ", it is characterized in that: will be to
The rail head top surface temperature of processing is that 650~900 DEG C of turnout rail carries out accelerating cooling to obtain the turnout rail of full pearlitic structrure,
Wherein, the acceleration cooling velocity of the rail head working side of turnout rail is higher than the acceleration cooling velocity of the rail head non-working side of turnout rail,
Its cooling velocity difference is 0.1~1.0 DEG C/s.It is especially non-to rail that rail head two sides cooling velocity difference is proposed in the patent
Symmetric cross-section rail property improve and flatness control bring benefit, but not yet explicitly the arrangement mode of different phase nozzle with it is cold
But influence of the speed to performance after heat-treatment of rail.
In the prior art for heat-treatment of rail be concentrated mainly on the different cooling within the scope of different temperatures control come
The control for realizing heat treatment procedure, is not directed to the Precise control of different spray nozzles arrangement mode and injection method, thus cannot
Obtain the excellent pearlite steel rail of obdurability.
Summary of the invention
The technical problem to be solved in the present invention are as follows: the prior art mostly uses the side of different cooling within the scope of different temperatures
Formula is heat-treated rail, obtained pearlite steel rail performance bad problem.
The technical solution of present invention solution technical problem are as follows: a kind of manufacturing method of traumatic resistance rail is provided.This method
The following steps are included:
A, steel rail rolling
By hot rolling of steel billet at rail, finishing temperature is 900~1000 DEG C；
B, the first stage is cooling
When rail surface central temperature is air-cooled to 800~850 DEG C, to rail head top surface, rail head two sides and rail head two sides
Lower jaw is blown cooling medium, and being cooled to end face center temperature is 540~570 DEG C；
C, second stage is cooling
Stop being blown rail head two sides lower jaw, continues to be cooled to rail to rail head top surface, rail head two sides blowing cooling medium
After head skin temperature is 460~500 DEG C, it is air-cooled to room temperature.
Wherein, in the manufacturing method of above-mentioned traumatic resistance rail, rail constituent described in step a are as follows: by weight
Percentages, C:0.70%~0.85%, Si:0.65%~0.90%, Mn:0.60%~1.10%, Cr:0.05%~
0.40%, at least one of V, Nb, Ti, the V of when containing V are 0.02%~0.10%, and the Ti of when containing Ti is 0.001%~0.030%,
The Nb of when containing Nb is 0.005%~0.08%, and surplus is Fe and inevitable impurity.
Wherein, in the manufacturing method of above-mentioned traumatic resistance rail, step b, the cooling medium described in c be compressed air or
At least one of water mist gaseous mixture.
Wherein, in the manufacturing method of above-mentioned traumatic resistance rail, step b, the cooling velocity described in c is 2.0~5.0
℃/s。
The present invention also provides a kind of traumatic resistance rail, constituents are as follows: by weight percentage, C:0.70%~
0.85%, Si:0.65%~0.90%, Mn:0.60%~1.10%, Cr:0.05%~0.40%, in V, Nb, Ti at least
One kind, the V of when containing V are 0.02%~0.10%, and the Ti of when containing Ti is 0.001%~0.030%, the Nb of when containing Nb for 0.005%~
0.08%, surplus is Fe and inevitable impurity.
Compared with prior art, the invention has the benefit that the present invention selects the rail of specific composition ingredient, by adopting
Accelerate cooling mode with two-part, compare existing single heat treatment mode, the pearlite steel rail of preparation has superior
Intensity, hardness, toughness and plasticity index, especially obdurability are substantially better than existing method.The method of the present invention is easy to operate, if
Standby of less demanding, the traumatic resistance rail of preparation can integrally improve the tough comprehensive performance at rail head position, effectively extend same
Under the conditions of rail service life.
Specific embodiment
The present invention provides a kind of manufacturing methods of traumatic resistance rail, comprising the following steps:
A, steel rail rolling
By hot rolling of steel billet at rail, finishing temperature is 900~1000 DEG C；
B, the first stage is cooling
When rail surface central temperature is air-cooled to 800~850 DEG C, to rail head top surface, rail head two sides and rail head two sides
Lower jaw is blown cooling medium, and being cooled to end face center temperature is 540~570 DEG C；
C, second stage is cooling
Stop being blown rail head two sides lower jaw, continues to be cooled to rail to rail head top surface, rail head two sides blowing cooling medium
After head skin temperature is 460~500 DEG C, it is air-cooled to room temperature.
Traumatic resistance rail of the present invention, constituent are as follows: by weight percentage, C:0.70%~
0.85%, Si:0.65%~0.90%, Mn:0.60%~1.10%, Cr:0.05%~0.40%, in V, Nb, Ti at least
One kind, the V of when containing V are 0.02%~0.10%, and the Ti of when containing Ti is 0.001%~0.030%, the Nb of when containing Nb for 0.005%~
0.08%, surplus is Fe and inevitable impurity.
C is the element that pearlite steel rail improves strong hardness, promotes perlitic transformation most important, most cheap.In item of the present invention
Under part, as C content < 0.70%, after heat treatment strong hardness is lower for rail, it is difficult to meet high axle load heavy haul railway abrasiveness
It can demand；As C content > 0.85%, even if accelerating cooling after finish to gauge, secondary cementite will be precipitated in grain boundaries, deteriorate steel
The toughness plasticity of rail.Therefore, C content is limited to 0.70%~0.85%.
Si is present in ferrite and austenite the intensity for improving tissue as the solution strengthening element in steel, meanwhile, it can
Proeutectoid cementite is inhibited to be precipitated, to improve the toughness plasticity of rail.Under the conditions of the present invention, as Si content < 0.65%,
Solid solution capacity is relatively low to cause strengthening effect unobvious；As Si content > 0.90%, the toughness plasticity of rail will be reduced, deteriorate rail
Lateral performance.Therefore, Si content is limited to 0.65%~0.90%.
Mn can form solid solution with Fe, improve the intensity of ferrite and austenite.Meanwhile Mn is that carbide forms member again
Element, into cementite after can partially substitute Fe atom, increase the hardness of carbide, the final hardness for increasing steel.In item of the present invention
Under part, as Mn content < 0.60%, strengthening effect is not significant, is only capable of improving the performance of steel slightly；When
When Mn content > 1.10%, carbide excessive high hardness in steel, toughness plasticity is substantially reduced；Meanwhile Mn influences Carbon diffusion in steel
Significantly, even if under the conditions of air-cooled, still there may be the abnormal structures such as B, M for the segregation zones Mn.Therefore, Mn content is limited to 0.60%
Between~1.10%.
Cr can form a variety of carbide as medium carbide former, with the carbon in steel；Meanwhile in the uniform steel of Cr energy
Distribution of carbides reduces carbide size, improves the abrasion resistance properties of rail.Under the conditions of the present invention, when Cr content is lower than
When 0.05%, the carbide hardness and ratio of formation are lower, and are assembled with sheet form, it is difficult to improve the wear resistance of rail
Energy；When chromium content be higher than 0.40%, easily form coarse carbide, deteriorate the toughness plasticity of rail.Therefore, Cr content is limited to
0.05%~0.40%.
When V is under room temperature, the solubility in steel is very low, and is such as present in austenite grain boundary in the hot rolling
Or other regions, be precipitated in V carbonitride (V (C, the N)) form of micronized particles shape, or with the compound precipitation of Ti in steel, inhibit
The growth of austenite grain, so that reaching refinement crystal grain proposes high performance purpose.Under the conditions of the present invention, when V content is lower than
When 0.02%, Carbonitride Precipitation containing V is limited, it is difficult to play strengthening effect；As V content > 0.10%, easily formed coarse
Carbonitride deteriorates the toughness plasticity of rail.Therefore, V content is limited to 0.02%~0.10%.
Austenite grain when main function of the Ti in steel is refinement heating, rolling and cooling, it is final to increase prolonging for rail
Stretch rate and rigidity.As Ti content < 0.001%, the carbide quantity formed in rail is extremely limited.In condition of the present invention
Under, as Ti content > 0.030%, on the one hand since Ti is strong carbonitride-forming elements, the TiC of generation is on the high side will to make rail
Excessive high hardness；On the other hand, TiN, TiC are on the high side is enriched with segregation to form coarse carbide, not only reduces toughness plasticity, also makes steel
Rail contact surface under impact loading is easy to crack and cause to be broken.Therefore, Ti content is limited to 0.001%~0.030%
Between.
Main function of the Nb in steel is similar to V, by the Nb carbonitride fining austenite grains of precipitation, and by
The carbonitride that roller repairing process generates, which generates precipitation strength, also can be improved the tough of rail while improving rail hardness
Plasticity, at the same Nb to prevent welding point softening also benefit.Under the conditions of the present invention, as Nb content < 0.005%, contain Nb
Carbonitride Precipitation is limited, it is difficult to play strengthening effect；As Nb content > 0.08%, coarse carbonitride is easily formed, is disliked
Change the toughness plasticity of rail.Therefore, Nb content is limited to 0.005%~0.08%.
The smelting process of the above-mentioned rail rail smelting process common using this field, will meet the steel of mentioned component requirement
Liquid continuous casting enters in heating furnace for cooling after 250mm × 250mm~450mm × 450mm section steel billet is heated to 1200~1300
DEG C and held for some time after come out of the stove, use omnipotent method or pass method to roll after high pressure water dephosphorization to be disconnected needed for 50~75kg/m
Face rail.
The mode being heat-treated at present to rail mainly carries out acceleration cooling to the rail head position of austenitizing rail,
And cooling nozzles are mainly arranged in the top surface and two sides at rail head of rail position, this is determined by the handling characteristics of rail: steel
The top surface of rail and one side bear the multi-phase complex stress from wheel, and rail is vertically symmetric cross-section, by
In the difference of installation site, two sides may be respectively subjected to wheel stress effect.Therefore, rail head top surface and two sides are to be on active service
The rail property at position should be higher than that the other positions of rail.
Accelerate in cooling procedure in existing rail head top surface and two sides, with the rapid drawdown of skin temperature, comes from rail head of rail
The heat of center portion and surface layer heat exchange, in heat transfer process, with the release of pearlitic transformation latent heat, rail head surface performance is not only
It will not reduce, may increase instead, this means that the reduction of rail head center portion phase transformation degree of supercooling, finally not only rail head at room temperature
The hardness of center portion is significantly lower than surface layer, and toughness is equally lower.The present invention increases by using in-orbit both sides of head lower jaw position sprays
The mode of mouth blowing cooling medium since rail head center portion and the cooling rate difference on rail head surface layer are reducing, may be used also during heat treatment
Keep the starting temperature of transformation on rail head surface layer lower, rail obdurability will further improve, although the amplitude of this raising is limited
, but obdurability this kind of for pearlite heat-treated rail have been approached the limit steel for be still conducive to tough comprehensive performance
It is promoted.
In the present invention, rail is cooled down in two stages, the first segment stage is to " rail head top surface, rail head two sides
With rail head two sides lower jaw " it is cooled down, it is cooling with the cooling temperature of 2.0~5.0 DEG C/s when rail is air-cooled to 800~850 DEG C
To 540~570 DEG C.Cooling can obtain more uniform thermo parameters method in this way, and provide item for subsequent phase transformation
Part.If grain refining effect is not significant when 2.0 DEG C/s of cooling rate <, it is difficult to achieve the purpose that obdurability Synchronous lifting；If cooling rate >
When 5.0 DEG C/s, then the abnormal structures such as B, M are easily formed, it is cooled due to accelerating after accelerating cooling especially with rail head lower jaw
The reduction of rail head center portion and web of the rail position to rail head surface layer heat supplement ability, is more likely formed abnormal structure in journey.Therefore, this hair
It is bright to set 2.0~5.0 DEG C/s for cooling velocity.
When rail head end face center temperature is down to 540~570 DEG C, the cooling of second stage is carried out.Stop rail head lower jaw to add
Quickly cooling but, only accelerates cooling to rail head top surface, rail head two sides, it is basic to be primarily due to rail head surface layer phase transformation in the temperature range
It completes, rail head center portion is in phase transition process, spot segregation position is equally increased even if applying biggish cooling rate at this time
The risk that abnormal structure is formed.Therefore, second stage it is cooling be cooled to after 460~500 DEG C with 2.0~5.0 DEG C/s continue it is air-cooled
To room temperature.Within this temperature range, the phase transformation of rail head of rail position is completed, and obtains finished product through processes such as subsequent aligning, flaw detection, processing
Rail.
Explanation will be further explained to a specific embodiment of the invention by embodiment below, but do not indicated this
The protection scope of invention is limited in range described in embodiment.
The rail that Examples 1 to 6 is manufactured with the method for the present invention
Rail steel billet chemical component used in Examples 1 to 6 is as shown in table 1 below:
The chemical component table (%) of 1 rail steel billet of table
| C | Si | Mn | P | S | Cr | V/Ti/Nb | |
| Embodiment 1 | 0.77 | 0.69 | 0.78 | 0.012 | 0.004 | 0.22 | 0.08V |
| Embodiment 2 | 0.70 | 0.74 | 1.10 | 0.013 | 0.003 | 0.10 | 0.014Ti |
| Embodiment 3 | 0.82 | 0.65 | 0.60 | 0.014 | 0.004 | 0.37 | 0.02V |
| Embodiment 4 | 0.85 | 0.88 | 0.64 | 0.010 | 0.003 | 0.40 | 0.02Nb |
| Embodiment 5 | 0.72 | 0.90 | 0.85 | 0.011 | 0.005 | 0.28 | 0.025Ti |
| Embodiment 6 | 0.80 | 0.80 | 0.93 | 0.010 | 0.006 | 0.05 | 0.005Nb |
Steel billet as shown above is rolled as 75kg/m rail, is cooled down in the following manner:
A, steel rail rolling
By hot rolling of steel billet at rail, finishing temperature is 900~1000 DEG C；
B, the first stage is cooling
When rail surface central temperature is air-cooled to 800~850 DEG C, to rail head top surface, rail head two sides and rail head two sides
Lower jaw is blown cooling medium, and being cooled to end face center temperature is 540~570 DEG C；
C, second stage is cooling
Stop being blown rail head two sides lower jaw, continues to be cooled to rail to rail head top surface, rail head two sides blowing cooling medium
After head skin temperature is 460~500 DEG C, it is air-cooled to room temperature.
The cooling velocity of Examples 1 to 6 is as shown in table 2 below.
Requirement of 2 distinct methods of table to cooling velocity
Comparative example 1~6 prepares pearlite steel rail using existing method
The same Examples 1 to 6 of steel billet constituent used by comparative example 1~6, the steel billet of comparative example 1 are embodiment 1, according to
This analogizes, and corresponds to each other.
Comparative example 1~6 is carried out using the existing type of cooling, is only situated between to rail head top surface and the blowing cooling of rail head two sides
Matter is air-cooled to room temperature after being cooled to 460~500 DEG C of rail head surface layer.
The cooling velocity that comparative example 1~6 is arranged is as shown in table 3:
Requirement of 3 distinct methods of table to cooling velocity
By embodiment and comparative example, treated that rail is air-cooled to room temperature, respectively below the rail head surface layer of rail 10mm,
D is taken at 30mm0=10mm, l0=5d0Round both shoulders tensile sample detects R according to GB/T 228.1 respectivelyp0.2、Rm, A, Z, in phase
10mm × 10mm × U-shaped impact specimen of 55mm Charpy is taken with position, ballistic work is tested according to GB/T 229.In addition, intercepting respectively
Rail head of rail position lateral stiffness sample, respectively apart from rail head surface layer 10mm, 30mm upside fillet and end face center position
Rockwell hardness is measured according to GB/T 230.1, embodiment and comparative example use identical test position and test method, as a result in detail
It is shown in Table 4 and table 5.
The mechanics property of rail (10mm below rail head surface layer) of 4 distinct methods of table preparation
The mechanics property of rail (30mm below rail head surface layer) of 5 distinct methods of table preparation
From above-described embodiment and comparative example: the present invention has chosen with identical chemical component, using of the present invention
The comparative example of the embodiment of heat treatment process and existing heat treatment process compares.Embodiment accelerates cooling side using two stages
Formula is blown cooling using rail head top surface+rail head two sides+rail head two sides lower jaw when waste heat rail is air-cooled to 800~850 DEG C jointly
The mode of medium is cooled to after rail head end face center temperature is 540~570 DEG C with the cooling rate of 2.0~5.0 DEG C/s and is stopped under rail head
Jaw accelerates cooling, until rail head end face center temperature continues to be air-cooled to room temperature after being down to 460~500 DEG C.In contrast, existing work
Skill uses the single heat treatment mode in rail head top surface+two sides of 2.0~5.0 DEG C/s of cooling rate.Comparing result table in table 4 and table 5
Bright, intensity, hardness, toughness and plasticity under technique of the present invention below rail head surface layer in 10mm are slightly above comparative example；More
Importantly, the toughness and tenacity below rail head surface layer at 30mm is apparently higher than existing heat treatment technics, it is seen that increase rail head lower jaw
Accelerate cooling that can integrally improve the tough comprehensive performance at rail head position, effectively extends the service life of rail under equal conditions.
In conclusion traumatic resistance rail and its production method in the present invention use under identical component and production technology
This method can make rail obtain more excellent obdurability index, and product is applicable in fatigue defect railway outstanding.
Claims (3)
1. the preparation method of traumatic resistance rail, which comprises the following steps:
A, steel rail rolling
By hot rolling of steel billet at rail, finishing temperature is 900~1000 DEG C；The rail constituent are as follows: by weight percentage
Meter, C:0.70%~0.85%, Si:0.65%~0.90%, Mn:0.60%~1.10%, Cr:0.05%~0.40%, V,
At least one of Nb, Ti, the V of when containing V be 0.02%~0.10%, the Ti of when containing Ti be 0.001%~0.030%, when containing Nb Nb
It is 0.005%~0.08%, surplus is Fe and inevitable impurity；
B, the first stage is cooling
When rail surface central temperature is air-cooled to 800~850 DEG C, to rail head top surface, rail head two sides and rail head two sides lower jaw
It is blown cooling medium, being cooled to end face center temperature is 540~570 DEG C；The speed of the cooling is 2.0~5.0 DEG C/s；
C, second stage is cooling
Stop being blown rail head two sides lower jaw, continues to be cooled to rail head table to rail head top surface, rail head two sides blowing cooling medium
After layer temperature is 460~500 DEG C, it is air-cooled to room temperature；The speed of the cooling is 2.0~5.0 DEG C/s.
2. the preparation method of traumatic resistance rail according to claim 1, it is characterised in that: step b, cold described in c
But medium is at least one of compressed air or water mist gaseous mixture.
3. the traumatic resistance rail of method preparation as claimed in claim 1 or 2, it is characterised in that: constituent are as follows: percentage by weight
Than counting, C:0.70%~0.85%, Si:0.65%~0.90%, Mn:0.60%~1.10%, Cr:0.05%~0.40%,
V, at least one of Nb, Ti, the V of when containing V are 0.02%~0.10%, and the Ti of when containing Ti is 0.001%~0.030%, when containing Nb
Nb is 0.005%~0.08%, and surplus is Fe and inevitable impurity.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201710934078.4A CN107675082B (en) | 2017-10-10 | 2017-10-10 | Traumatic resistance rail and its manufacturing method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201710934078.4A CN107675082B (en) | 2017-10-10 | 2017-10-10 | Traumatic resistance rail and its manufacturing method |
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| CN115466834A (en) * | 2022-08-26 | 2022-12-13 | 包头钢铁（集团）有限责任公司 | Heat treatment method for producing U71MnH steel rail by adopting water mist cooling medium |
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| CN102220545B (en) * | 2010-04-16 | 2013-02-27 | 攀钢集团有限公司 | High-carbon and high-strength heat-treated steel rail with high wear resistance and plasticity and manufacturing method thereof |
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