CN106103772A - Rail and manufacture method thereof - Google Patents

Rail and manufacture method thereof Download PDF

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Publication number
CN106103772A
CN106103772A CN201580013144.3A CN201580013144A CN106103772A CN 106103772 A CN106103772 A CN 106103772A CN 201580013144 A CN201580013144 A CN 201580013144A CN 106103772 A CN106103772 A CN 106103772A
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Prior art keywords
rail
rolling
deviation
length direction
cooling
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CN106103772B (en
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木村达己
高岛由纪雄
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JFE Steel Corp
JFE Engineering Corp
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NKK Corp
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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
    • 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
    • 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
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • 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
    • 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

Abstract

The present invention provides a kind of hardness deviation suppressing rail length direction and the rail that ensure that excellent mar proof.This rail has following component composition: containing C:0.60～1.0%, Si:0.1～1.5%, Mn:0.01～1.5%, below P:0.035%, below S:0.030% and Cr:0.1～2.0%, surplus is made up of Fe and inevitable impurity, and the deviation of the case hardness of this rail length direction is for below ± HB15 point.

Description

Rail and manufacture method thereof
Technical field
The present invention relates to rail, particularly relate to the little rail of the deviation of high rigidity and hardness and manufacture method thereof.
Background technology
For goods conveying, mine railway, owing to Weight Loaded is than passenger vehicle weight, the therefore load of the axletree of lorry Greatly, the contact environment between rail and wheel is very harsh.As the rail for this environment, it is desirable to have mar proof, mesh Before, use the steel with pearlitic structrure.
In recent years, in order to railway transportation is efficient, goods, the Weight Loaded increase further etc. of mineral, the abrasion of rail It is further exacerbated by, the rail replacement lost of life.Therefore, in order to extend the replacing life-span of rail, it is desirable to improve the wear-resistant of rail Property, it is proposed that the high rigidity rail of multiple raising rail hardness.
For example, at patent document the 1st, patent document the 2nd, patent document 3 and Patent Document 4 discloses and make the carburizing scale of construction increase Hypereutectoid rail and manufacture method.In addition, at patent document the 5th, patent document 6 and Patent Document 7 discloses by right The technology that the steel of eutectoid carbon grade makes the stratiform of pearlitic structrure be spaced miniaturization and realizes high rigidity.
With regard to the manufacture method of rail, patent document 8 proposes excellent high-strength of the internal fatigue failure of a kind of head The manufacture method of degree rail, it is characterised in that in the rolling of rail steel disc, at head surface temperature 850 DEG C～1050 DEG C Carry out retaining the finish rolling of final finish rolling, more than 3 seconds and after passage interval time of less than 1 minute, in head surface temperature Carry out the final finish rolling of 1 passage or multi-pass with reduction ratio below 10% for every a time at spending 800 DEG C～950 DEG C, then, Begin to cool down the acceleration cooling of speed 2～4 DEG C/sec between 0.1～10 second, will be less than 5mm's under the surface in head and corner Temperature is cooled to Ar1Below transformation temperature, then the maximum cooling velocity with surface is more than 4 DEG C/sec and less than 30 DEG C/sec cold But speed cools down.
Showing the manufacture method of a kind of high tenacity rail presenting pearlite metal structure in patent document 9, it is special Levy and be, the steel disc roughing of the carbon steel or low alloy steel containing C:0.60～1.00% is become rail shape, then at this rail Surface temperature be that implement the cross section of 3 passage each of the above passages between 850～1000 DEG C to reduce reduction ratio be 5～30% roll The continuous finish rolling of system, and rolling pass is spaced apart less than 10 seconds, then naturally cools down or with 2～15 DEG C/sec from more than 700 DEG C Temperature be cooled between 700～500 DEG C.
In addition, Patent Document 10 discloses a kind of mar proof and the manufacture of the excellent perlite rail of ductility Method, it is by terms of quality %, containing C:0.65～1.20%, Si:0.05～2.00%, Mn:0.05～2.00%, And the steel rail rolling steel disc that is made up of Fe and inevitable impurity of surplus at least carries out roughing and finish rolling manufactures wear-resistant Property and the method for the excellent perlite rail of ductility, it is characterised in that in described finish rolling, on rail's end portion surface be Less than 900 DEG C～Ar3The accumulation contraction percentage of area carrying out head within the scope of temperature more than transformation temperature or Arcm transformation temperature is More than 20% and reaction force than for more than 1.25 rolling, described reaction force ratio is to remove with the counterforce values of rolling mill With value obtained from the counterforce values at the identical accumulation contraction percentage of area and rolling temperature 950 DEG C, then, after finish rolling Rail's end portion surface is accelerated cooling with cooling velocity 2～30 DEG C/sec or naturally cools at least 550 DEG C.
For goods conveying, mine railway be main body high axle weight Rail for railway for, in order to improve the durable of rail Property and require the rail of excellent in wear resistance, propose the rail towards various high rigidity as mentioned above.
Prior art literature
Patent document
Patent document 1: No. 4272385 publications of Japanese Patent No.
Patent document 2: No. 3078461 publications of Japanese Patent No.
Patent document 3: No. 3081116 publications of Japanese Patent No.
Patent document 4: No. 3513427 publications of Japanese Patent No.
Patent document 5: No. 4390004 publications of Japanese Patent No.
Patent document 6: Japanese Unexamined Patent Publication 2009-108396 publication
Patent document 7: Japanese Unexamined Patent Publication 2009-235515 publication
Patent document 8: No. 3423811 publications of Japanese Patent No.
Patent document 9: No. 3113137 publications of Japanese Patent No.
Patent document 10: Japanese Unexamined Patent Publication 2008-50687 publication
Content of the invention
Invention problem to be solved
But, rail carries out hot rolling to steel raw material and manufactures, and its length reaches more than 100m, because of manufacture method not Same, have hardness deviation at rail length direction, can not play fully owing to producing uneven wear sometimes when laying Effect.Therefore, the deviation of the hardness reducing mill length direction is extremely important, but with regard to the deviation of this hardness, above-mentioned Patent document 1～10 does not all have any record.
Therefore, it is an object of the invention to, propose a kind of hardness deviation suppressing rail length direction and guarantee excellent The rail of mar proof, and its manufacture method is proposed in the lump.
Solve the method for problem
Inventors etc. choose for rail abrasion examination from the steel with pearlitic structrure being equivalent to different hardness rail The test film tested, carries out wear test and have studied the relation of hardness and wear extent.Its result of study is shown in Fig. 1.
It should be noted that wear test uses the western former formula wear test that can evaluate mar proof at short notice Machine and simulate reality pearlitic steel rail and wheel contact conditions and as comparative test.That is, as in figure 2 it is shown, make from steel The western former formula wear test piece 1 of the external diameter 30mm that rail head portion chooses contacts with tire test piece 2 and rotates and test.This figure In arrow represent the direction of rotation of western former formula wear test piece 1 and tire test piece 2 respectively.Tire test piece is from JIS standard The head of the common rail that E1101 records chooses the pole of diameter 32mm, and Brinell hardness (Brinell loads 29.4kN) is HB370, carries out heat treatment and makes tissue become tempered martensite, is then carried out processing, is processed as the shape shown in Fig. 2, Make tire test piece.It should be noted that western former formula wear test piece 1 is as shown in Figure 3 from two position choosings of rail's end portion 3 Take.The test film that top layer from rail's end portion 3 is chosen is set to western former formula wear test piece 1a, the test film will chosen from inside It is set to western former formula wear test piece 1b.The length direction of the western former formula wear test piece 1b choosing from the inside of rail's end portion 3 It is centrally located at the degree of depth of upper surface 24～26mm (mean value 25mm) away from rail's end portion 3.Experimental enviroment condition is drying regime, At contact: 1.2GPa, sliding ratio (slip ratio) :-10%, rotating speed: 750rpm's (tire test piece is 750rpm) Under the conditions of measure rotation 1.8 × 105Wear extent after Zhuaning.Test film weight before and after determination test, goes out according to its mathematic interpolation Wear extent.
As it is shown in figure 1, with the rising of hardness, mar proof improves.For example, when the hardness of rail is more than HB400, with General heat-treated rail (HB370) is compared, and mar proof can be made to improve 15%.But, the hardness of rail length direction When deviation is bigger, at hard part and soft part, difference can be produced on abrasional behavior.For example, when HB415 point, hardness is inclined In the case that difference is for less than ± 15 (discrete in the scope of more than HB400 and below HB430), the change of wear extent is from 0.37g Being changed to 0.3g, therefore the deviation of wear extent is within 20%.On the other hand, it is contemplated that when HB415 point hardness deviation for ± During the situation of 30 (discrete in the scope of more than HB385 and below HB445), the change of wear extent is changed to from 0.40g 0.27g, therefore the deviation of wear extent also becomes 33%.Accordingly, due to rail in use by contacting with wheel And wear and tear, therefore preferably try one's best uniformly worn out at length direction, reduced rail by the high rigidity with rail It at the hardness deviation of length direction, is capable of the uniform wear of rail, is favorably improved rail life.In view of above-mentioned abrasion Test it was found that the hardness deviation of preferred rail length direction is the wear extent deviation within 20%, make case hardness Deviation for, within ± HB15, it may thereby be ensured that excellent mar proof along its length, being favorably improved rail life, from And complete the present invention.
That is, the purport of the present invention is as follows.
(1) a kind of rail, it has following component and forms: in terms of quality %, contain
C:0.60～1.0%,
Si:0.1～1.5%,
Mn:0.01～1.5%,
Below P:0.035%,
Below S:0.030% and
Cr:0.1～2.0%,
Surplus is made up of Fe and inevitable impurity,
Wherein, the case hardness deviation of the rail's end portion of this rail length direction is for below ± HB15 point.
Here, the case hardness deviation of rail length direction refers to, along mill length direction with 5m spacing to full length rail (such as 25～100m) measures the Brinell hardness at rail head top, and the mean value calculating according to measurement result and each measuring point The difference of ball hardness number.That is, rail case hardness deviation along its length refers to, between with 5m below for ± HB15 point Away from measure whole hardness measurements (situation of total length 25m be 6 points, the situation of total length 50m be 11 points, the situation of total length 100m It is the measured value of 21) obtain the mean value of Brinell hardness, this mean value is maximum with the difference of the Brinell hardness for each measuring point Within ± 15.It should be noted that when measuring Brinell hardness, removing the de-of more than 0.5mm in advance with grinder etc. It is measured after carbon-coating.
(2) rail described in above-mentioned (1), wherein, described one-tenth is grouped in terms of quality %, possibly together with a kind or 2 in following More than Zhong,
Below Cu:1.0%,
Below Ni:0.5%,
Below Mo:0.5% and
Below V:0.15%.
(3) above-mentioned (1) or (2) described in rail, wherein, the case hardness of described rail's end portion is more than HB400.
(4) rail according to any one of above-mentioned (1)～(3), wherein, the deviation of described case hardness for ± HB10 point with Under.
(5) manufacture method of a kind of rail, the method includes: steel raw material is heated to more than 1200 DEG C, is then carried out Hot rolling and manufacture rail,
In described hot rolling, the temperature range below 1000 DEG C carries out including rolling of multiple passage along rail length direction System, within being set to the deviation of passage interval time of rail length direction when carrying out this rolling 15 seconds, will become rail The accumulation contraction percentage of area of the part of head is set to more than 40% and final rolling temperature is set to more than 900 DEG C, after this hot rolling Continue to carry out cooling beginning temperature to rail's end portion: more than 800 DEG C, cooling stopping temperature: less than 600 DEG C and cooling velocity: 1～ The cooling of 10 DEG C/sec,
Described steel raw material has following component composition: in terms of quality %, contain
C:0.60～1.0%,
Si:0.1～1.5%,
Mn:0.01～1.5%,
Below P:0.035%,
Below S:0.030% and
Cr:0.1～2.0%,
Surplus is made up of Fe and inevitable impurity.
(6) manufacture method of the rail described in above-mentioned (5), wherein, becomes to be grouped in terms of quality %, in following It is one kind or two or more,
Below Cu:1.0%,
Below Ni:0.5%,
Below Mo:0.5% and
Below V:0.15%.
(7) above-mentioned (5) or (6) described in the manufacture method of rail, wherein, in described cooling, by rail length direction The deviation of cooling velocity be set to ± less than 1 DEG C/sec.
The effect of invention
According to the present invention it is possible to make the hardness deviation of rail length direction very little, especially for parcel railway, It is extremely effective that the durability of the rail laid in mine railway contour axle weight environment improves (long lifetime) aspect, industrially sends out Wave remarkable result.
Brief description
Fig. 1 is the chart of the relation with wear extent for the hardness illustrating rail material.
Fig. 2 is the figure illustrating the western former formula wear test piece evaluating mar proof, and (a) is top view, and (b) is side view.
Fig. 3 is the rail's end portion profile of the chosen position illustrating western former formula wear test piece.
Detailed description of the invention
First, the restriction reason of each composition in being grouped into the one-tenth of rail below is described.It should be noted that only Without special instruction, the meaning of " % " expression " quality % " in composition.
C:0.60～1.0%
C (carbon) is to form cementite in pearlite steel rail and improve hardness, intensity, thus improves the important of mar proof Element.But, these DeGrains when less than 0.60%, are therefore 0.60% by lower limit set.On the other hand, although C The increase of amount means the increase of the carburizing scale of construction, can expect the increase of hardness, intensity, but, ductility reduction.In addition, C amount Increase make γ+theta temperature expanded range, the softening of welding heat affected zone can be promoted.In view of these impacts, the upper limit of C is set It is set to 1.0%.Preferably in the range of 0.73～0.85%.
Si:0.1～1.5%
Si (silicon) is the deoxidation material as rail material, and is used for making equilibrium phase change temperature (TE) raise and strengthen pearl Light soma (hardness that the miniaturization of lamellar tissue causes increase) and add, but when less than 0.1%, these effects are relatively Little.On the other hand, therefore the upper limit is set as 1.5% by the generation increasing the surface defect promoting decarburization, promotion rail of Si. It is preferably the scope of 0.5～1.3%.
Mn:0.01～1.5%
Mn (manganese) has makes the pearlitic transformation temperature of reality reduce and make the effect of pearlite stratiform interval densification, is to use In the effective element reaching high rigidity, but when less than 0.01%, its effect is less.On the other hand, owing to quenching also can be made Property improve, therefore add more than 1.5% when easily become bainite, martensite mutually, therefore the upper limit is set as 1.5%.Preferably It is the scope of 0.3～1.2%.
Below P:0.035%
If P (phosphorus) is more than 0.035%, then toughness, ductility reduction.Therefore, the upper limit of P is set as 0.035%.Make It for preferred scope, is set as the upper limit by 0.025%.On the other hand, for lower limit, owing to can lead when carrying out special refining etc. Causing melting cost increases, and is therefore preferably set to 0.001%.
Below S:0.030%
S (sulphur) is formed at the thick MnS that rolling direction stretches, and makes ductility, toughness reduce.Therefore, upper by the content of S Limit is set as 0.030%.On the other hand, when less than 0.0005%, cost when melting processes the melting such as time increase is notable Increasing, therefore preferred lower limit is 0.0005%.It is preferably 0.001～0.015%.
Cr:0.1～2.0%
Cr (chromium) makes equilibrium phase change temperature (TE) raise and contributes to the miniaturization at pearlite stratiform interval, makes hardness, strong Degree increases.Accordingly, it would be desirable to add more than 0.2%.On the other hand, when adding more than 2.0%, sending out of weld defect can not only be increased Raw, and increase hardenability, promote the generation of martensite, therefore, the upper limit is set as 2.0%.More preferably 0.26～ The scope of 1.00%.
In addition to above-mentioned chemical composition, can also add below Cu:1.0%, below Ni:0.5%, Mo:0.5% with One kind or two or more in lower and below V:0.15%.
Below Cu:1.0%
Cu (copper) can be by solution strengthening and realizes the element of further high rigidity.In addition, for suppression decarburization Also effective.In order to obtain this effect, preferably with 0.01% interpolation carried out above.On the other hand, add more than 1.0% continuously During casting, rolling when easily produce face crack, therefore preferably the upper limit is set as 1.0%.In addition, be still more preferably The scope of 0.05～0.6%.
Below Ni:0.5%
Ni (nickel) is to raising toughness, the effective element of ductility.Further, since be to pressing down by add compound with Cu The effective element of Cu crackle processed, therefore preferably adds Ni in the case of adding Cu.But, when less than 0.01%, it is impossible to really Recognize these effects, therefore, in the case of adding, be preferably more than 0.01% by lower limit set.On the other hand, interpolation exceedes 0.5% can improve hardenability and promote the generation of martensite, therefore preferably the upper limit is set as 0.5%.More preferably 0.05～ The scope of 0.50%.
Below Mo:0.5%
Mo (molybdenum) is effective element for high intensityization, and when less than 0.01%, its effect is less, preferably sets lower limit It is set to 0.01%.On the other hand, interpolation more than 0.5% when, hardenability improve, result can generate martensite so that toughness, Ductility reduces terrifically.Therefore, the upper limit is preferably set to 0.5%.The scope of more preferably 0.05～0.30%.
Below V:0.15%
V (vanadium) forms VC or VN etc. and separates out imperceptibly in ferrite, is to be helped by ferritic precipitation strength Element in high intensity.In addition, the solid solubility temperature of VC or VN is substantially lower than Ti and Nb, to tying again of austenite during rolling The impact that brilliant behavior causes is also little, and therefore, the impact causing the characteristic deviation of rail length direction is also little.And then, also conduct The capture site of hydrogen and play a role, can expect to suppress the effect of delayed fracture.It is therefore preferable that it is carried out above with 0.001% Add.On the other hand, interpolation more than 0.15% when, above-mentioned each effect is saturated, and the increase of cost of alloy is very big, and therefore the upper limit is excellent Choosing is set as 0.15%.The scope of more preferably 0.005～0.12%.
It should be noted that the balance of Fe beyond above-mentioned composition and inevitable impurity.
For example, as inevitable impurity, N can allow to 0.006%, and O can allow to 0.003%.In addition, Al Although being effective as deoxidation material, but the tufted AlN of shape can be substantially reduced rolling contact fatigue (rolling fatigue) spy Property, it is therefore preferable that Al is set as less than 0.003%.In addition, with regard to Nb and Ti containing as inevitable impurity, As described below.
Below Nb:0.003%
Below Ti:0.003%
Nb (niobium) and Ti (titanium) form carbide or carbonitride and strengthen matrix, are therefore to improving hardness, wear-resistant The effective element of property.But, be harmful element of the hardness deviation promoting rail length direction, therefore substantially without, But as the amount being unavoidably mixed into, less than 0.003% can be allowed.That is, when adding Nb, Ti, heat according to raw material, roll System or cooling condition and make the change of hardness increase, therefore can be sensitively to the mill length direction of these condition deviations adjoint Firmness change impacts.It is believed that in terms of metallurgy, while promoting the inhomogeneities of heating austenite grain, suppression Recrystallizing and bigger very than the steel without Nb, Ti with the change of this pearlitic transformation temperature accompanying of austenite in rolling Many, therefore promote the deviation of hardness.
In addition to above-mentioned one-tenth is grouped into, it is important to make the case hardness deviation of rail length direction for ± HB15 point with Under.Its reason is, hardness deviation exceed ± HB15 point when, the change of rail abrasion amount reaches more than 20%.If it is in addition, hard The deviation of degree is for below ± HB10 point, so that it may so that the change of rail abrasion amount is less than 15%, therefore more preferably rail length side To the deviation of case hardness for ± HB10 point below.
Then, the manufacturing condition of rail is specifically described.
For steel raw material, slab being preferably used as steel raw material, described slab is to utilize blast furnace, iron The smelting process techniques such as water pretreatment, converter, RH degassing, and use continuous casting process to enter the molten steel being adjusted to mentioned component composition Obtained from row casting.
By conventional groove rolling (caliber rolling), universal rolling (universal rolling) to this steel Raw material carry out hot rolling, are thus shaped to rail shape.Hereinafter, to heating now, rolling condition, with and subsequent cooling The restriction reason of condition illustrates.
[heating-up temperature before hot rolling: more than 1200 DEG C]
The steel raw material of melting needs to be heated to more than 1200 DEG C.Here, main purpose is to reduce deformation by abundant Resistance and mitigate rolling load, its purpose also reside in realization homogenization.In order to obtain these effects fully, needing will heating temperature Degree is set as more than 1200 DEG C.It should be noted that the upper limit does not needs to set especially, but de-from suppression oxide skin loss, suppression It from the viewpoint of carbon, is preferably set to less than 1300 DEG C.
[when the temperature range below 1000 DEG C carries out the rolling of multiple passage along rail length direction, by rail length Within the deviation setting of passage interval time in direction is 15 seconds]
Steel raw material heated as mentioned above is shaped to rail shape by hot rolling, now, it is critical that In the rolling of less than the 1000 DEG C multi-pass carrying out, by being repeated between the passage that the rolling in a direction is reduced in rolling The deviation of interval.It should be noted that the passage in Zha Zhi refers to (roll from the length direction of steel rail rolling material interval time Direction processed) certain part roll of nipping rise to the time of next roll of nipping.And, this passage interval time is at steel rail rolling The top (front end) of material and bottom (tail end) difference are maximum.
In addition, in the case of conventional reverse rolling, for rolling top (front end), stinging from certain passage roll Enter to next passage and started time of nipping, owing to next passage is that (tail end) starts to be sequentially sent to roll bottom rolling The form of roller, the passage therefore rolling top extends interval time.On the other hand, due to rolling bottom (tail end) pass through certain passage Afterwards in next passage first by roll of nipping, therefore passage shortening interval time.Before such reverse rolling is specific The difference of passage interval time of end and tail end can affect austenite structure state, affects the hardness deviation after pearlitic transformation.Phase Under Bi, when continuous rolling in one direction, the difference of passage interval time of rolling stock front end and tail end is substantially very little. Therefore, it can eliminate the inhomogeneities of the austenite structure being produced by above-mentioned passage difference interval time.Thus, it is desirable to by this road Within the difference of minor tick time is set as 15 seconds.That is, as long as within the difference of passage interval time being set as 15 seconds, with regard to energy Enough suppress the hardness deviation of rail length direction.Within being preferably 12 seconds.
Above-mentioned restriction applies to the condition of the rolling carrying out below 1000 DEG C in hot rolling, represents in roughing operation For the rolling of the temperature range more than 1000 DEG C of property, it is possible to use inversely roll.In a word, as long as can in a direction even The continuous rolling carrying out less than 1000 DEG C, then the rolling in the temperature range more than 1000 DEG C of its leading portion is arbitrary.In hot rolling The rolling carrying out below 1000 DEG C is preferably carried out with 2～7 passages.This is because, for 1 passes, rolling is negative Carry and increase and be difficult to moulding, whereas if more than 7 passages, then have that the state of austenite is somewhat uneven and the deviation of hardness The tendency increasing.
[the accumulation contraction percentage of area becoming the part of rail's end portion is set as more than 40%]
In terms of accumulation, need the contraction percentage of area caused for the rolling of less than 1000 DEG C is set as more than 40%.This is Owing in order to promote the recrystallization grain refined of austenite, needing to carry out the section shrinkage processing of more than 40% below 1000 DEG C. In the case that the contraction percentage of area of the rolling below 1000 DEG C is less than 40%, the recrystallization grain refined of austenite is insufficient, office The thick austenite of portion's remaining, result makes the hardness deviation of rail length direction (rolling direction) increase.
[final rolling temperature: more than 900 DEG C]
When the deviation by carrying out passage interval time that continuous rolling reduces rolling stock total length in one direction, Preferably final rolling temperature is set as more than 900 DEG C.This is because, when final rolling temperature is less than 900 DEG C, because continuing to implement after rolling The cooling of burning optimization on line start temperature low temperature, promote the reasons such as pearlitic transformation (high temperature), hardness integrally reduces, partially Difference increases.In order to prevent such hardness from reducing, preferably final rolling temperature is set as more than 900 DEG C.
And then, continue under conditions of the following stated, carry out cooling process after above-mentioned hot rolling.
" carry out cooling at rail's end portion and start temperature: more than 800 DEG C, cooling stop temperature: less than 600 DEG C, cool down fast Degree: the cooling of 1～10 DEG C/sec "
First, cooling beginning temperature is preferably more than 800 DEG C.That is, when cooling starts temperature less than 800 DEG C, it is impossible to fill Divide and guarantee degree of supercooling, have the hidden danger that can not obtain enough case hardnesses.Cooling stops temperature being needed into walking to less than 600 DEG C. This is because enough hardness cannot be obtained when more than 600 DEG C.Lower limit is not particularly limited, even if but owing to being cooled to Less than 400 DEG C hardness also can be saturated, and hinders productivity because cool time extends, and therefore preferably stops more than 400 DEG C Cooling.
Cooling velocity is the scope of 1～10 DEG C/sec.When cooling velocity is more than 10 DEG C/sec, it is impossible to substantially ensure that pearlite phase Become time, can bainite, martensite and make toughness, ductility, fatigue failure reduce.On the other hand, less than 1 DEG C/ Enough hardness cannot be obtained during the second.It is preferably the scope of 2～8 DEG C/sec.
Additionally, it is preferred that make the cooling velocity in mill length direction deviation be less than ± 1 DEG C/sec.This is because, pass through The deviation making cooling velocity is less than ± 1 DEG C/sec, can reduce the deviation at pearlite stratiform interval further, is capable of hard The deviation of degree is ± below HB10, reduces deviation along rail length direction further in terms of mar proof, endurance destructiveness.
In addition, the cooling proceeding after above-mentioned hot rolling preferably carries out air blast cooling or misting cooling.Here, air blast is cold But refer to by forcing blows air to be accelerated cooling to rail's end portion.In addition, misting cooling refers to mix water and air Merge and make water become vaporific to rail's end portion winding-up.
In order to the cooling velocity of controlled rolling length direction makes deviation less, for example, in the case of air-blast cooled, need With the Separation control air pressure of below 5m (preferably below 3m), carry out inclined with the temperature of the rail length direction cooling down pre-test online The regulation of the corresponding air pressure of difference, is constant cooling velocity in length direction control.The situation of misting cooling is excellent similarly The water yield of selected control length direction, pressure cool down.
Becoming be grouped into and roll and cool down by above, the case hardness that can obtain rail length direction is preferably More than HB400, its deviation for ± HB15 point below and at the little uniform high rigidity pearlite of mill length direction hardness deviation Steel rail.
Embodiment
Melting has the steel of the chemical composition shown in table 1, to carrying out heating by casting the slab obtaining continuously, hot rolling, It is then carried out cooling, thus manufactured the rail of 136 pounds or 141 pounds respectively.By its manufacturing condition, case hardness and deviation thereof Result of study is shown in table 2 in the lump.
Here, the deviation of the passage interval time under rolling condition refers to, from the front end of rolling stock rolled under The time being once rolled and tail end from rolling stock be rolled to the difference of the time being rolled next time.As described above, In the conventional rolling utilizing reverse rolling, the passage at rolling top extends interval time, on the other hand, and road bottom rolling The minor tick time shortens.So, in reverse rolling, during the road minor tick of the front end (top) of rolling stock and tail end (bottom) Between difference more apparent.By contrast, when continuous rolling in one direction, between rolling stock front end and the adjoint passage of tail end The subtractive of interval is little, therefore can eliminate the inhomogeneities of the tissue of generation, and this situation is as shown in table 2.
In addition, cooling starts temperature and stopping temperature is with thermoviewer (thermoviewer) measurement rail corner Surface temperature obtained from result.It for the cooling velocity of rail, is cold according to length direction 5m distance measurement But start temperature, cooling stops temperature and cool time, and measurement cooling velocity simultaneously makes obtained from its equalization.On the other hand, For the cooling velocity deviation of length direction, whether the difference of the maxima and minima obtaining each cooling velocity deviation is big In ± 1 DEG C/sec or for less than ± 1 DEG C/sec.
In addition, for the rail manufacturing, have rated case hardness and the microstructure of its head.For rail's end portion surface Hardness for, utilize grinder remove more than 0.5mm decarburized layer, the point in the 5m spacing of rail length direction measures cloth respectively Family name's hardness.Similarly cut out microscope example, observe microstructure.
These evaluation results are shown in table 2.
According to the rail of the present invention, the hardness deviation of its length direction is minimum, is ± below HB15, by contrast, for Becoming for being grouped into the rail departing from the scope of the present invention with any one in rolling condition, the deviation of its hardness exceeded ± HB15。

Claims (7)

1. a rail, it has following component and forms: in terms of quality %, contain
C:0.60～1.0%,
Si:0.1～1.5%,
Mn:0.01～1.5%,
Below P:0.035%,
Below S:0.030% and
Cr:0.1～2.0%,
Surplus is made up of Fe and inevitable impurity,
Wherein, the case hardness deviation of the rail's end portion of this rail length direction is for below ± HB15 point.
2. rail according to claim 1, wherein, described one-tenth is grouped in terms of quality %, possibly together with a kind in following or Two or more,
Below Cu:1.0%,
Below Ni:0.5%,
Below Mo:0.5% and
Below V:0.15%.
3. rail according to claim 1 and 2, wherein, the case hardness of described rail's end portion is more than HB400.
4. the rail according to according to any one of claims 1 to 3, wherein, the deviation of described case hardness for ± HB10 point with Under.
5. a manufacture method for rail, the method includes: steel raw material is heated to more than 1200 DEG C, be then carried out hot rolling and Manufacture rail,
In described hot rolling, the temperature range below 1000 DEG C carries out including the rolling of multiple passage along rail length direction, Within the deviation of passage interval time of rail length direction when carrying out this rolling is set to 15 seconds, rail's end portion will be become The accumulation contraction percentage of area of part be set to more than 40% and final rolling temperature be set to more than 900 DEG C, continue after this hot rolling Rail's end portion is carried out cooling start temperature: more than 800 DEG C, cooling stopping temperature: less than 600 DEG C and cooling velocity: 1～10 DEG C/sec cooling,
Described steel raw material has following component composition: in terms of quality %, contain
C:0.60～1.0%,
Si:0.1～1.5%,
Mn:0.01～1.5%,
Below P:0.035%,
Below S:0.030% and
Cr:0.1～2.0%,
Surplus is made up of Fe and inevitable impurity.
6. the manufacture method of rail according to claim 5, wherein, described one-tenth is grouped in terms of quality %, possibly together with under One kind or two or more in stating,
Below Cu:1.0%,
Below Ni:0.5%,
Below Mo:0.5% and
Below V:0.15%.
7. the manufacture method of the rail according to claim 5 or 6, wherein, in described cooling, by rail length direction The deviation of cooling velocity is set to ± less than 1 DEG C/sec.
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