CN102534387A - Bainite/martensite steel rail with 1,500 Mpa level of high toughness and manufacturing method thereof - Google Patents
Bainite/martensite steel rail with 1,500 Mpa level of high toughness and manufacturing method thereof Download PDFInfo
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Abstract
The invention provides a bainite/martensite steel rail and a manufacturing method thereof. The steel rail is formed by performing steel hot rolling on the following components in percentage by weight: 0.10 to 0.40 percent of C, 0.80 to 2.00 percent of Si, 1.20 to 2.40 percent of Mn, 0.50 to 1.20 percent of Cr, 0.20 to 0.60 percent of Mo, and the balance of Fe and inevitable impurities. The steel rail comprises a rail head, a rail waist and a rail bottom, wherein the rail head is subjected to accelerated cooling at a cooling speed of higher than 1 DEG C/s and lower than and equal to 5 DEG C/s to an accelerated cooling stop temperature of lower than 300 DEG C and higher than 200 DEG C.
Description
Technical field
The present invention relates in general to the rail field, relates in particular to bainite/martensite rail and method of manufacture thereof.
Background technology
In recent years, along with train speed, axle is heavy and the increase of traffic density, rail defects and failures is serious day by day, especially on parts such as sharp radius curve or point tongue or wing rail, rail wear, peel off and abrade very serious.Especially, on sharp radius curve, some rail use less than 1 year, through gross weight less than hundred million tons, just because of the replacing of having to of transfiniting of rail head side wear; It is also very serious that the rail level of the gauge angle of thigh rail and following strand rail peels off piece in curve circuit, and the rail upper track time that has is not long, and rail level peels off piece and just reaches several millimeters, even also brings out tired severe injury, causes the rail cross break.In addition, in starting location and the down hill braking location of going up a slope, engine burn also happens occasionally, and causes disconnected rail when serious, influences safety of railway transportation and efficient.
In order to reduce the abrasion of rail, the available technology adopting multiple means, normally alloying or alloying and heat treatment phase bonded mode, the intensity and the hardness that improve rail are to improve wear resisting property.For example:
1) in steel, increases C, Si component content, and add alloys such as V, Cr, do not add the microalloy rail of other processing after rolling, like U75V shaped steel rail etc.
2) the rail head sclerosis heat-treated rail through quickening to make at cooling rail head position is like U75V, U77MnCr, PG4 heat-treated rail etc. the Chinese patent ZL96117731.4 of the heat treating method of vanadium-containing alloy rail by name (for example referring to).
3) C content to the hypereutectoid composition in the increase steel; Adopt the mode that increases cementite density to increase its wear resisting property; Quicken cooling (being online thermal treatment) both refine pearlite tissue, raising hardness through full section again; Suppress separating out of free cementite again, with the so-called hypereutectoid heat-treated rail that guarantees to have enough toughness plasticities (for example referring to the patent ZL96190344.9 of " rail of wearability and anti-inner hurt excellent property and the method for manufacture thereof " by name of Nippon Steel Manufacturing Corp; And the patented claim 03800576.X of " pearlite steel rail that wear resistance and ductility are good and method of manufacture thereof " by name etc.).
Yet above-mentioned rail is characterised in that its C content is all above more than 0.70%, and weave construction is perlite.For pearlite steel rail; Adopt alloying and heat treatment phase bonded mode to make intensity reach the 1300MPa level basically near the limit; If improve intensity again, just be difficult to avoid to appear at not allowing high-carbon fragility (sheet or the twin) martensitic stucture that exists under this high-carbon content situation.In addition, C content is high more in the steel, and the alloy of interpolation is many more, and hardening capacity is strong more, and the abrasive ability of opposing locomotive wheel was also poor more during rail used.
The contriver finds that under the effect repeatedly of wheel Rail Contact Stresses, material generation viscous deformation and distortion accumulate, exhaust producing with post-hardening, plasticity and peel off crackle that crack propagation causes falling piece in the Wheel territory usually; Obviously to fall the ability of piece favourable to improving antistripping for the plasticity index that improves material thus.
Peeling off the piece hurt for the rail rail level, is a kind of solution with the regular rail grinding of large-scale polishing train.The expensive but it is not only polished, and during train operation, often do not have the sufficient polishing time.
To problem and other problem that above-mentioned pearlite steel rail exists, bainite class rail arises at the historic moment.
For example; Angang New Steel Co., Ltd. discloses a kind of meta-bainite rail in the patent of invention ZL02158853.8 that it is by name " resistance to wear, high-strong toughness meta-bainite rail and method of manufacture " thereof; It is through the steel that alloying is provided and the rail after making hot rolling elder generation air cooling to 400 ℃ again slowly cools to 200 ℃ with the low speed of cooling of 0.01 ℃/s-0.002 ℃/s; And then air cooling acquisition meta-bainite rail, its rail tissue is carbide-free Bainite basically.
The rail that Beijing Special Metallurgy Industry &. Trade Co., Ltd. discloses a kind of bainitic steel and processed with this steel in the patented claim 201010275470.0 of its by name " curve and heavily loaded rail are with bainitic steel and bainite rail and working method thereof ", this rail are through alloying and complete heat treatment subsequently and be cooled to 350-300 ℃ in the acceleration of the speed of cooling of 10-20 ℃/s and also carry out ageing treatment at last.
Above-mentioned bainite rail, its tensile strength grade are roughly 1200 or the 1300MPa level, and the tread surface hardness is 370 or the 380HB rank, though its toughness plasticity is superior to the pearlite type rail, wear resisting property is not as good as the pearlite type rail of same intensity grade.And above-mentioned patent or patented claim require the full section of rail is heat-treated (or cooling), and hope in the full section of rail, to form consistent hardness (for example seeing summary of the invention final stage among the ZL02158853.8).And in rail, be desirable to provide sufficiently high rail head of rail surface hardness usually; And provide suitable hardness to be fit to steel rail straightening and the bore operation in laying in other part of rail.Thus, the rail of above-mentioned documents is difficult to realize this effect.
Summary of the invention
Therefore, the present invention is directed to the problems referred to above, a kind of high-strong toughness bainite/martensite rail and method of manufacture thereof of the 1500MPa of having level is provided.This bainite/martensite rail significantly is lower than at C content under the situation of above-mentioned pearlite steel rail, control meticulously its constituent content (being alloying) with and treatment process make the structural constituent of rail head be low relatively bainite of C content and lath martensite have excellent resistance to wear, anti-ly peel off, antifraying property.
In a scheme of the present invention; A kind of bainite/martensite rail is provided; This rail comprises rail head, the web of the rail and the flange of rail and by containing C:0.10-0.40% by % (weight), Si:0.80-2.00%, Mn:1.20-2.40%; Cr:0.50-1.20%; Mo:0.20-0.60%, and can contain one or more elements that are selected from down group as required: Ni:0.10-2.00%, Cu:0.05-0.50%, V:0.03-0.15%, RE:0.01-0.05%, and surplus is the steel hot rolling formation of iron and unavoidable impurities.And; This rail head is keeping high temperature or is being reheated to the pyritous situation after the hot rolling, from the austenite region temperature (to be preferably greater than 1 ℃/s and to quicken to be cooled to less than 300 ℃ smaller or equal to 3 ℃/s) speed of cooling but stop temperature greater than 200 ℃ acceleration cooling greater than 1 ℃/s and smaller or equal to 5 ℃/s.
According to another aspect of the present invention; A kind of method of manufacture of bainite/martensite rail correspondingly is provided; It comprises: provide by % (weight) and contain C:0.10-0.40%, Si:0.80-2.00%, Mn:1.20-2.40%; Cr:0.50-1.20%; Mo:0.20-0.60%, and can contain one or more elements that are selected from down group as required: Ni:0.10-2.00%, Cu:0.05-0.50%, V:0.03-0.15%, RE:0.01-0.05%, and surplus is the steel of iron and unavoidable impurities; This steel hot rolling is formed rail with rail head, the web of the rail and flange of rail; With keep high temperature after the hot rolling or reheated to the rail head of pyritous rail (to be preferably greater than 1 ℃/s and smaller or equal to 3 ℃/s) speed of cooling greater than 1 ℃/s and smaller or equal to 5 ℃/s; So that it quickens to be cooled to less than 300 ℃ from the austenite region temperature but stop temperature accomplishing structural transformation greater than 200 ℃ acceleration cooling, thereby in this rail head, form bainite and martensitic stucture.Further, rail head can naturally cooling after quickening cooling or spray cooling to normal temperature.
And for without quickening other position of refrigerative, the for example web of the rail and the flange of rail can air cooling (naturally cooling) to normal temperature (envrionment temperature in other words); Perhaps also can adopt other suitable cooling way.
And according to a preferred embodiment of the invention, can also after rail head (and other part) cooling, carry out further thermal treatment again.Such as; Utilize rolling waste heat and quicken the refrigerative rail head and the rail of all the other position air coolings for having, can after rail is cooled to normal temperature, reheat (tempering) again to 200 ℃-400 ℃; Be incubated 4-10 hour, naturally cool near normal temperature (or envrionment temperature) then.
The other preferred embodiment according to the present invention can also carry out needed thermal treatment before rail head quickens cooling.Such as; Reheated to high temperature and be accelerated the refrigerative rail subsequently for rail head; Before rail head quickens cooling (when for example reheating rail head); Can the web of the rail of this rail and the flange of rail be heated to 400-650 ℃ and be not incubated with the rate of heating of 3 ℃/s-10 ℃/s, this has realized the high temperature, short time tempered effect of the web of the rail and the flange of rail.
Before the steel hot rolling that rail according to the present invention is made up of said composition forms; Can also for example pass through converter smelting, external refining, vacuum outgas; The process bloom continuous casting is processed and is applicable to the hot rolled steel billet; But also can use other suitable means, this is well known in the art at this and is not described further.
The rail head position (for example in 20mm scope from outward appearance to inner essence) of the rail that makes according to above-mentioned rail of the present invention and according to aforesaid method not only has high intensity (tensile strength >=1500MPa) for example; Suitable high firmness (for example the tread surface hardness is 420-480HB); (for example also has good plasticity; And H.T. (ballistic work Ak >=40J) for example elongation A >=12%, relative reduction in area Z >=40%).In addition, handle to make the strength grade at positions such as the web of the rail, the flange of rail both be not less than 980MPa through optimization technique means of the present invention control heating and cooling, be not more than the 1400MPa level again, be convenient to steel rail straightening and lay use in operation such as boring.
The following inventor will combine above-mentioned technical scheme of the present invention to describe technique effect of the present invention and advantage.But it will be apparent to one skilled in the art that following description is indicative, but not require necessary described all technical characterictics of technical scheme of the present invention and/or effect, and the present invention does not get rid of other technique effect or the progress that realizes outside the hereinafter description.
Explanation to rail element of the present invention and content thereof:
C is the fundamental element in the steel.Be lower than 0.10% like C content, then be difficult to guarantee the hardness of rail; And when C content surpasses 0.40%, may in tissue, form the bigger twin crystal martensite of fragility, unfavorable to the toughness of rail.Therefore, C content should be controlled at 0.15-040%.
Si is the solution strengthening element, the element that carbide is separated out when suppressing bainite transformation especially in the present invention.Carbide in the bainite is existed with the paralympic mode of rich carbon, improve the toughness of air-cooled bainitic steels.When si content is lower than 0.80%, it is not enough to suppress the effect that carbide separates out; Be higher than at 2.00% o'clock, make the toughness variation of steel, so Si content is limited between 0.80～2.00%.
Mn can obviously postpone perlitic transformation, can improve the intensity and the hardness of steel simultaneously.When content less than 1.20% the time, effect is not enough; And surpass at 2.40% o'clock, and form the twin crystal martensite tissue easily in segregation place, worsen the toughness of steel.Therefore, limit Mn in 1.20～2.40% scopes.
Effect and the Mn of Cr are similar, have the effect of obvious postponement perlitic transformation, and the intensity of steel and hardness are improved.When Cr content was lower than 0.50%, then above-mentioned effect was not enough; Greater than 1.20% o'clock, can make the intensity of steel and hardness too high, be unfavorable for the aligning and the following process of rail, therefore, limit Cr in the 0.50-1.20% scope.
Mo can postpone perlitic transformation strongly, makes bainite transformation in advance, is the important element of bainitic steel, can make continuous cooled rail form the air-colled bainite tissue.When Mo content in the 0.30-0.50% scope, above-mentioned effect is just fairly obvious.Mo is valuable alloy, in order not only to play a role but also practice thrift cost, so limit Mo at 0.20-0.60% and preferably in the 0.30-0.50% scope.
Add Ni and can obviously improve the toughness of rail steel, and have effect paralympic in the stable bainitic steel.But when its content less than 0.10% the time, DeGrain; Surpass at 2.00% o'clock, also be difficult to strengthen again its effect.So limit Ni in the 0.10-2.00% scope.
Cu is a kind of toughness of not damaging steel, and can improve the element that its intensity increases corrosion resisting property simultaneously.Best results in the 0.05-0.50% scope surpasses 0.50% and work as content, then is prone to produce red brittleness, so limit Cu in the 0.05-0.50% scope.
V because V (C, separating out N) can be strengthened bainite structure, especially when adopting 850-950 ℃ of heating, when steel rail weld joint is carried out postweld heat treatment, but its performance of refinement welding joint tissue raising, but its content is undesirable in 0.03% effect when following; Content is 0.15% when above, and (C, N) thick and embrittlement is so be limited in 0.03～0.15% scope can to make V.
Steel through RE handles can make inclusion modification, increases the toughness of steel.The RE add-on generally is controlled at about 0.020%, and weak effect can form the toughness that re inclusion worsens steel too much on the contrary very little.
Acceleration refrigerative explanation to rail head:
The very important point is the acceleration cooling of controlling rail head meticulously in the present invention.For example; In the composition of afore mentioned rules; Especially in (for example in the scope of carbon at about 0.10%-about 0.40%) under the situation of relative low carbon content,, promptly begin bainite transformation at high-temperature area when with the time less than the speed cooling of 1 ℃/s; The bainite structure that forms is comparatively thick, and obdurability is not enough; When with the cooling of 5 ℃/ cooling rate more than the s, the undesirable position of some of rail hardness is too high, is unfavorable for aligning and following process.Therefore, hope that will speed up rail head refrigerative speed of cooling is limited to greater than 1 ℃/s and smaller or equal to 5 ℃/s, and preferably greater than 1 ℃/s and in smaller or equal to 3 ℃/s scope.And simultaneously, also hope will speed up under the speed of cooling of afore mentioned rules refrigerative stop temperature limitation less than 300 ℃ and greater than 200 ℃ scope in, can obtain the tissue of tiny bainite and lath martensite so wittingly, have good obdurability.
In addition, acceleration cooling of the present invention can use pressurized air as heat-eliminating medium, and pressurized air is for example by top side that is disposed at rail head of rail and the ejection of two side nozzles.And for spray cooling mentioned above, be that mist cools off through the atomizer ejection gas-vapor mix that is configured in the rail head end face for example.
In addition, " high temperature " in " reservation high temperature or quilt are reheated to high temperature after the hot rolling " of the present invention refers to such an extent that be the austenite region temperature TR of austenitizing in other words, and this is well known by persons skilled in the art.And the structural transformation of preceding text indication comprises that at least the preferred whole austenitic transformation of at least a portion of rail head is the bainite/martensite tissue, and the austenitic transformation of the preferred web of the rail and the flange of rail is a bainite.
To reheating the tempered explanation in the preferred version:
As stated, in the present invention, quicken under the refrigerative situation for the rail head with rolling waste heat, other positions of rail (the for example web of the rail and the flange of rail) can naturally cool to normal temperature usually continuously.In this case; Because cooling is not quickened at the web of the rail, flange of rail position; Therefore they tend under comparatively high temps, (to stop the temperature height than acceleration cooling of the present invention) bainite transformation take place, so wherein have more stable inadequately residual austenite even sheet or twin crystal martensite tissue, are improvement and stability; The present invention reheats to 200～400 ℃ the full section of rail, is incubated 4～10 hours Di to carry out temper.
And reheat with austenitizing and quicken the refrigerative rail subsequently again for rail head; The present invention had instructed before quickening cooling; Preferably when rail head reheats; To other position except that rail head, for example the flange of rail, web of the rail position are heated to 400～600 ℃ with the rate of heating of 3-10 ℃/s.This has realized the effect of high temperature, short time tempered, this both can be as above-mentioned improve and stability, can also simplify thermal treatment process simultaneously.For example, through such processing, tempering once more after rail head quickens cooling and the whole air cooling of rail.But can certainly be to such rail behind air cooling, complete again section is heated to 200-400 ℃, is incubated and 4-10 hour Di carries out temper, with the further performance of improving.
Through above-mentioned bainite/martensite rail and method of manufacture thereof provided by the invention with 1500MPa level high-strong toughness, its rail head through the martensite with tiny bainite and lath-shaped be suitable for heavy haul railway especially the used rail of sharp radius curve or track switch with the requirement of rail; Particularly to occurring on the curve strand rail or track switch with tongue or wing rail rail head side wear, rail head end face or gauge angular position peel off the scratch that piece and tread face cause because of locomotive skids and have very strong resistibility.
Description of drawings
Below, specify embodiments of the invention in conjunction with accompanying drawing, wherein:
Fig. 1 has shown the transverse section of the TB 60kg/m pattern rail that is used for embodiment;
Fig. 2 has shown the tension specimen sampling figure in the transverse section of rail shown in Figure 1;
Fig. 3 has shown the impact specimen sampling figure in the transverse section of rail shown in Figure 1;
Fig. 4 is the rail head transverse section hardness synoptic diagram according to embodiments of the invention 1;
Fig. 5 shows the metallographic structure according to the rail head position of embodiments of the invention 1;
Fig. 6 is the rail head transverse section hardness synoptic diagram according to embodiments of the invention 2;
Fig. 7 shows the metallographic structure according to the rail head position of embodiments of the invention 2;
Fig. 8 is the rail head transverse section hardness synoptic diagram according to embodiments of the invention 3;
Fig. 9 shows the metallographic structure according to the rail head position of embodiments of the invention 3;
Figure 10 is the full transverse section of the rail hardness synoptic diagram according to embodiments of the invention 2.
Embodiment
Fig. 1 has shown the transverse section of TB (railway systems standard) the 60kg/m pattern rail that is used for embodiments of the invention, and the pattern size of this rail is known, and it has rail head 100, the web of the rail 200 and the flange of rail 300 that limits the tread face that contacts with wheel.And stretching and ballistic sampling in order to show the rail transverse section in accompanying drawing 2-3, a plurality of dimensional parameters of in rail head, the web of the rail and the flange of rail, expressing respectively, and will be with reference to the regulation in the above-mentioned standard for all the other parameters that do not mark.In addition, although contrast with TB 60kg/m pattern rail between the rail and comparison rail of the embodiment of the invention, can expect that rail of the present invention and method of manufacture thereof are fit to the rail of multiple other pattern at this.
Described multiple hardness level in the present invention, for example HB (HB) and Rockwell hardness (HRC) can convert according to known reduction formula between them.And in the rail field, the tread surface hardness representes with HB that generally transverse section hardness representes with HRC that generally the present invention also follows such method for expressing generally.
Hereinafter is through relatively demonstration advantage of the present invention and improvement between a plurality of embodiment of the present invention and the existing comparative example rail.
Hereinafter table 1-1 is the embodiment 1 and chemical ingredients that compares rail and corresponding technological conditions (cooling and heat-treat condition) of rail of the present invention, and wherein chemical ingredients refers to wherein each elemental composition and the content of steel, and surplus is Fe and unavoidable impurities.Tempering Heating temperature among the embodiment 1 and tempering are meant the tempering temperature and the soaking time of heating cooling back rail head cross-section integral body heat-up time.
The chemical ingredients and the processing condition of the rail of table 1-1 embodiment 1 and the rail of comparative example
Show the test-results contrast of embodiment and comparative example among a plurality of figure hereinafter respectively.Wherein, table 1-2 is the full section stretch test result of rail of the present invention; Table 1-3 is the full section impact property test-results of the embodiment 1 of rail of the present invention; Table 1-4 is the stretch test result of rail comparative example; Table 1-5 is the Impulse Test Result of the rail comparative example of pearlite type; Table 1-6 is the rail head stretch test result contrast of the rail comparative example of rail of the present invention and pearlite type; Table 1-7 is the full section impact property contrast of the rail comparative example of rail of the present invention and pearlite type.Hereinafter and other place in full, as do not have special indicating then: R
mRefer to tensile strength, R
P0.2Refer to that ys, A refer to that elongation, Z refer to relative reduction in area.
In addition, the test of embodiments of the invention and comparative example all with Fig. 2 or 3 label take a sample accordingly, and come comparison with the arithmetical av of corresponding site (rail head, the web of the rail or the flange of rail) sampling.
The rail tensile property of table 1-2 embodiment 1
The full section impact property of rail of table 1-3 embodiment 1
The rail head stretch test result of the rail of table 1-4 comparative example
The full section Impulse Test Result of the rail of table 1-5 comparative example
Table 1-6 embodiment 1 contrasts with the rail tensile property of comparative example
| Rail type | Rm/MPa | R p0.2/MPa | A/％ | Z/ |
| Embodiment | ||||
| 1 | 1530 | 1245 | 14.0 | 58.0 |
| Comparative example 1 | 1365 | 863 | 11.3 | 36.0 |
| Comparative example 2 | 1260 | 788 | 13.8 | 40.8 |
| Comparative example 3 | 1145 | 675 | 12.0 | 27.8 |
| |
1.12 | 1.44 | 1.24 | 1.61 |
| |
1.21 | 1.58 | 1.01 | 1.42 |
| |
1.34 | 1.84 | 1.17 | 2.09 |
Table 1-7 embodiment 1 contrasts with the impact property of the rail of comparative example
Can know that by above-mentioned comparing result the tensile strength at the rail head position of the rail of embodiments of the invention 1 improves 12%-34% than the rail of the comparative example of pearlite type; Elongation improves 1%-24%; Relative reduction in area improves 42%-109%; The rail head ballistic work be pearlite type comparative example rail 2.6-3.5 doubly; The web of the rail is 5.5-7.8 times; The flange of rail is 3.1-4.3 times.
And be about 42HRC-48HRC from the hardness (scope from tread towards interior 20mm) in the rail head transverse section of the embodiment of the invention shown in Figure 41, this compares with comparative example 1 and is significantly improved.In Fig. 4 and Fig. 6 afterwards and 8, the numeral that is shown for this some place be the hardness value of unit with HRC, adjacent point-to-point transmission be spaced apart 3mm.In addition, can also see the metallographic structure figure at rail head position from Fig. 5.Need to prove at this; The 20mm scope from outward appearance to inner essence of the rail head in this article scope from tread towards interior 20mm in other words refers to the set of the closest range of the middle distance tread face in the transverse section at the point of about 20mm; Wherein, The tread face is known in this area, and it refers in xsect, is positioned at the connected head-to-tail arc section of multistage between 1: 20 oblique line section of both sides.
In addition, although not shown, the tread mask of embodiment 1 has the hardness of 420-480HB.
Be similar to the foregoing description 1, table 2-1 is the embodiment 1 and the chemical ingredients and the corresponding technological conditions that compare rail of rail of the present invention.In embodiment 2, through reheating austenitizing, and the tempering temperature of the embodiment 2 that is shown among the table 2-1 is meant that the web of the rail and the flange of rail are with the tempering range that speed was heated to of 3-10 ℃/s when the heating rail head to rail head before quickening cooling.
Table 2-1 rail of the present invention and the chemical ingredients and the processing condition that compare rail
Similarly, table 2-2 is the full face stretch test result of rail of embodiment 2; Table 2-3 is the full section impact property of the rail test-results of embodiment 2; Table 2-4 be that the rail head of rail stretch test result of comparative example of rail and the pearlite type of embodiment 2 contrasts; Table 2-5 be that the full section impact property of rail of comparative example of rail and the pearlite type of embodiment 2 contrasts.Wherein, just identical among the chemical ingredients of the comparative example 1-3 in present embodiment and embodiment 3 and heat-treat condition and the embodiment 1.
Can find out by following form, the tensile strength at the rail head of rail position of embodiments of the invention 2 than pearlite type comparative example rail improve 17%-39%, elongation raisings-6%-15%, relative reduction in area improve 23%-80%, rail head ballistic work be the comparative example rail 3.2-4.8 doubly, the web of the rail be 3.0-4.3 doubly, the flange of rail is 2.2-3.0 times.
And with reference to figure 6 and Figure 10, it shows present embodiment 2 rail head of rail transverse section and full face hardness test result respectively.In the rail head transverse section, the hardness in the from outward appearance to inner essence about 20mm scope of rail head is in this embodiment in about about 48HRC scope of 44HRC-.Fig. 7 shows the metallographic structure figure of the rail head of embodiment 2.
The rail tensile property of table 2-2 embodiment 2
The full section Impulse Test Result of rail of table 2-3 embodiment 2
The rail of table 2-4 embodiment 2 and the rail tensile property contrast of comparative example
| Rail type | Rm/MPa | R p0.2/MPa | A/％ | Z/ |
| Embodiment | ||||
| 2 | 1595 | 1075 | 13.0 | 50.0 |
| Comparative example 1 | 1365 | 863 | 11.3 | 36.0 |
| Comparative example 2 | 1260 | 788 | 13.8 | 40.8 |
| Comparative example 3 | 1145 | 675 | 12.0 | 27.8 |
| |
1.17 | 1.25 | 1.15 | 1.39 |
| |
1.27 | 1.36 | 0.94 | 1.23 |
| |
1.39 | 1.59 | 1.08 | 1.80 |
The rail of table 2-5 embodiment 2 and the contrast of comparative example rail impact property
Be similar to the foregoing description, below through a plurality of forms and combine Fig. 8 and 9 that the improvement of the embodiment of the invention 3 than the comparative example rail is described.Table 3-1 is the chemical ingredients and the processing condition (thermal treatment and cooling conditions) of rail and the comparative example rail of embodiment 3.Table 3-2 is the rail head of rail stretch test result of embodiment 3.Table 3-3 is the rail head of rail impact property test-results of embodiment 3.Table 3-4 is the comparative example rail head of rail stretch test result contrast of rail and the pearlite type of embodiment 3.Table 3-5 is rail and the contrast of comparative example rail head of rail impact property of embodiment 3.Fig. 8 shows present embodiment 2 rail head of rail transverse section hardness test results.Fig. 9 shows the metallographic structure figure of the rail head of embodiment 3.
Can know that by following and accompanying drawing result the tensile strength at the rail head of rail position of embodiment 3 improves 17%-39%, elongation raising-6%-15%, relative reduction in area raising 23%-80% than comparative example rail; The rail head ballistic work be the comparative example rail 3.2-4.8 doubly, the web of the rail be 3.0-4.3 doubly, the flange of rail be 2.2-3.0 doubly.Hardness in the from outward appearance to inner essence about 20mm scope of rail head is in about 44HRC-48HRC scope.
The rail of table 3-1 embodiment 3 and the chemical ingredients and the processing condition of comparative example rail
The tensile property of the rail head of the rail of table 3-2 embodiment 3
The rail head position Impulse Test Result of table 3-3 embodiment 3
The rail of table 3-4 embodiment 3 and the rail head tensile property contrast of comparative example rail
| Rail type | Rm/MPa | R p0.2/MPa | A/％ | Z/ |
| Embodiment | ||||
| 3 | 1585 | 1065 | 14.5 | 52.0 |
| Comparative example 1 | 1365 | 863 | 11.3 | 36.0 |
| Comparative example 2 | 1260 | 788 | 13.8 | 40.8 |
| Comparative example 3 | 1145 | 675 | 12.0 | 27.8 |
| |
1.16 | 1.23 | 1.28 | 1.44 |
| |
1.26 | 1.35 | 1.28 | 1.27 |
| |
1.38 | 1.58 | 1.21 | 1.87 |
The rail of table 3-5 embodiment 3 and the rail head impact property contrast of comparative example rail
Although the invention describes a plurality of embodiment, the applicant does not plan scope of the present invention is confined to or is restricted in any form these details.After reading disclosure of the present invention, advantage of the present invention is readily understood that to those skilled in the art with improving, therefore can under the situation that does not break away from desired thought of the present invention of applicant and scope, makes a change.Scope of the present invention is not to confirm with reference to above-mentioned explanation, and should be with reference to appending claims and be equal to confirm.
Claims (10)
1. a bainite/martensite rail is characterized in that, this rail is by containing C:0.10-0.40% by % (weight); Si:0.80-2.00%, Mn:1.20-2.40%, Cr:0.50-1.20%; Mo:0.20-0.60%, surplus is that the steel hot rolling of iron and unavoidable impurities forms; This rail comprises from the austenite region temperature to quicken to be cooled to less than 300 ℃ greater than 1 ℃/s and smaller or equal to the speed of cooling of 5 ℃/s but stop the rail head of temperature greater than 200 ℃ acceleration cooling, and this rail also comprises the web of the rail and the flange of rail.
2. rail according to claim 1 is characterized in that, said steel contains C:0.10-0.40% by % (weight); Si:0.80-2.00%; Mn:1.20-2.40%, Cr:0.50-1.20%, Mo:0.20-0.60%; And one or more elements that are selected from down group: Ni:0.10-2.00%, Cu:0.05-0.50%, V:0.03-0.15%, RE:0.01-0.05%, surplus is iron and unavoidable impurities.
3. rail according to claim 1 and 2 is characterized in that, forms in martensite and bainite structure and/or the said web of the rail and the flange of rail in the rail head of said rail and forms bainite structure.
4. rail according to claim 1 and 2; It is characterized in that; The rail head of said rail is in 20mm scope from outward appearance to inner essence; Have tensile strength more than or equal to 1500MPa, the elongation greater than 12%, the relative reduction in area greater than 40% and greater than the ballistic work of 40J, and other positions of rail have the tensile strength of 980MPa-1300MPa, said rail head has the tread face that hardness is 420-480HB.
5. the method for manufacture of a bainite/martensite rail is characterized in that, comprising:
Provide by % (weight) and contain C:0.10-0.40%, Si:0.80-2.00%, Mn:1.20-2.40%, Cr:0.50-1.20%, Mo:0.20-0.60%, surplus is the steel of iron and unavoidable impurities;
This steel hot rolling is formed rail with rail head, the web of the rail and flange of rail;
With keep high temperature after the hot rolling or reheated to the rail head of pyritous rail with greater than 1 ℃/s and smaller or equal to the speed of cooling of 5 ℃/s, so that it quickens to be cooled to less than 300 ℃ from the austenite region temperature but stops temperature this rail head, to form bainite and martensitic stucture greater than 200 ℃ acceleration cooling.
6. method according to claim 5 is characterized in that, also comprises the steps:
For keeping high temperature and rail head after the hot rolling to quicken the refrigerative rail greater than 1 ℃/s and smaller or equal to the speed of cooling of 5 ℃/s, reheat again to 200 ℃-400 ℃, be incubated 4～10 hours, naturally cool to normal temperature then.
7. method according to claim 5 is characterized in that, also comprises the steps:
Reheated to the pyritous rail for rail head, before rail head quickens cooling, the web of the rail of this rail and the flange of rail are heated to 400-650 ℃ and be not incubated with the rate of heating of 3 ℃/s-10 ℃/s.
8. according to each described method in the claim 5 to 7, it is characterized in that, also be included in after rail head quickens cooling, make the step of rail head naturally cooling or spray cooling to normal temperature.
9. according to each described method in the claim 5 to 7, it is characterized in that said speed of cooling is greater than 1 ℃/s and smaller or equal to 3 ℃/s.
10. according to each described method in the claim 5 to 7, it is characterized in that said steel contains C:0.10-0.40% by % (weight); Si:0.80-2.00%; Mn:1.20-2.40%, Cr:0.50-1.20%, Mo:0.20-0.60%; And one or more elements that are selected from down group: Ni:0.10-2.00%, Cu:0.05-0.50%, V:0.03-0.15%, RE:0.01-0.05%, surplus is iron and unavoidable impurities.
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| CN2011104110543A CN102534387A (en) | 2011-12-12 | 2011-12-12 | Bainite/martensite steel rail with 1,500 Mpa level of high toughness and manufacturing method thereof |
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| CN2011104110543A CN102534387A (en) | 2011-12-12 | 2011-12-12 | Bainite/martensite steel rail with 1,500 Mpa level of high toughness and manufacturing method thereof |
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| CN2011104110543A Pending CN102534387A (en) | 2011-12-12 | 2011-12-12 | Bainite/martensite steel rail with 1,500 Mpa level of high toughness and manufacturing method thereof |
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