CN103160736B - High-strength bainite steel rail and heat treatment process thereof - Google Patents
High-strength bainite steel rail and heat treatment process thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 50
- 239000010959 steel Substances 0.000 title claims abstract description 50
- 229910001563 bainite Inorganic materials 0.000 title claims abstract description 33
- 238000000034 method Methods 0.000 title abstract description 9
- 230000008569 process Effects 0.000 title abstract description 7
- 238000010438 heat treatment Methods 0.000 title abstract description 5
- 238000001816 cooling Methods 0.000 claims abstract description 39
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 17
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 15
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 10
- 238000005098 hot rolling Methods 0.000 claims abstract description 9
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 8
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 6
- 239000000126 substance Substances 0.000 claims abstract description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract 4
- 239000012535 impurity Substances 0.000 claims abstract 2
- 229910052742 iron Inorganic materials 0.000 claims abstract 2
- 238000007669 thermal treatment Methods 0.000 claims description 11
- 229910052719 titanium Inorganic materials 0.000 claims description 11
- 229910052720 vanadium Inorganic materials 0.000 claims description 10
- 239000000203 mixture Substances 0.000 claims description 6
- 150000001875 compounds Chemical class 0.000 claims description 4
- 238000005096 rolling process Methods 0.000 abstract description 14
- 238000004519 manufacturing process Methods 0.000 abstract description 6
- 230000003111 delayed effect Effects 0.000 abstract description 2
- 238000003303 reheating Methods 0.000 abstract 1
- 239000011651 chromium Substances 0.000 description 19
- 239000011572 manganese Substances 0.000 description 19
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 14
- 239000010955 niobium Substances 0.000 description 13
- 229910000734 martensite Inorganic materials 0.000 description 12
- 230000000694 effects Effects 0.000 description 11
- 229910052758 niobium Inorganic materials 0.000 description 11
- 239000010936 titanium Substances 0.000 description 10
- 229910001566 austenite Inorganic materials 0.000 description 9
- 229910052799 carbon Inorganic materials 0.000 description 9
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 9
- 230000009466 transformation Effects 0.000 description 9
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 6
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 6
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 6
- 229910000859 α-Fe Inorganic materials 0.000 description 6
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 5
- 229910045601 alloy Inorganic materials 0.000 description 4
- 239000000956 alloy Substances 0.000 description 4
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- 238000005275 alloying Methods 0.000 description 3
- 229920001296 polysiloxane Polymers 0.000 description 3
- 230000009467 reduction Effects 0.000 description 3
- 238000005204 segregation Methods 0.000 description 3
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 2
- 238000004458 analytical method Methods 0.000 description 2
- 230000005540 biological transmission Effects 0.000 description 2
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- 239000011733 molybdenum Substances 0.000 description 2
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- 230000033764 rhythmic process Effects 0.000 description 2
- 239000010703 silicon Substances 0.000 description 2
- 229910000617 Mangalloy Inorganic materials 0.000 description 1
- 230000015556 catabolic process Effects 0.000 description 1
- BQKCOFRVVANBNO-UHFFFAOYSA-N chromium manganese Chemical compound [Cr][Mn][Cr] BQKCOFRVVANBNO-UHFFFAOYSA-N 0.000 description 1
- 230000000295 complement effect Effects 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
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- 229910000765 intermetallic Inorganic materials 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
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- 230000005501 phase interface Effects 0.000 description 1
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- 238000004881 precipitation hardening Methods 0.000 description 1
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Abstract
The invention provides a high-strength bainite steel rail and a heat treatment process thereof, wherein the steel rail comprises the following chemical components in percentage by weight: c: 0.10% -0.32%, Si: 0.80% -2.00%, Mn: 0.80% -2.80%, Cr: < 1.50%, Mo: 0.10% -0.40%, Ni: 0 to 0.5 percent of Mn + Cr +0.5Ni, less than or equal to 2.8 percent of Ni, and the balance of iron and inevitable impurities. After hot rolling the steel rail or air cooling the hot rolled steel rail to room temperature, reheating the steel rail to 850-1000 ℃ for austenitizing: cooling the rail head to 620-570 ℃ at a cooling rate of 0.3-15 ℃/s, cooling to 350-200 ℃ at a cooling rate of 0.5-5 ℃/s when the temperature is lower than 620-570 ℃, and then air-cooling to room temperature. The invention avoids excessive unstable coarse M-A islands generated in the granular bainite when the hot rolling air is cooled to room temperature, reduces the risk of straightening fracture (or delayed fracture) of the hot rolled steel rail, and improves the production process adaptability of steel grades. The tensile strength is more than 1400MPa, the best matching of the strength and the toughness and the plasticity is realized, and the rolling contact fatigue resistance and the wear resistance of the steel rail are excellent.
Description
Technical field
The present invention relates to a kind of railway track and manufacture thereof, particularly a kind of high strength bainite steel rail and thermal treatment process thereof.
Background technology
Along with the progress of railway heavy haul transport technology, China railways heavy haul transport ability is improving constantly, and existing passenger-cargo mixed transport line road year is very general more than 100,000,000 tons by gross train weight, and Freight Car Axle Load is progressively improving, and within 2008, Datong-Qinhuangdao Railway freight volume reaches 3.4 hundred million tons.Under this background, facilitate the exploitation of applicable heavy haul transport railway track.
Heavy haul transport peels off block and resistance to rolling contact fatigue performance is had higher requirement to rail is resistance to, and bainite rail meets this requirement with the resistance to rolling contact fatigue performance of its excellence just.This respect document has:
K.Sawley，J.Kristan，Development of bainitic rail steels with potentialresistance to rolling contact fatigue，Fatigue fract Engng Mater Struct 26，2003，1019-1029.
The bainite rail J6 introduced in document, hot rolled rail intensity rank reaches 1400MPa, and rail head unit elongation is only 5.0%, relative reduction in area 6.4%, and the plasticity of the web of the rail is lower, unit elongation 4.0-5.0%, relative reduction in area 2.8-5.9%.Although this rail intensity is higher, plasticity is too low, cannot meet the needs of railway operation safety.Trace it to its cause, mainly alloying element content is too high, especially the element M n2.00% of hardening capacity is improved, Cr1.94%, Mn+Cr reaches 3.94%, and the constituent content improving hardening capacity reaches so high level, can produce the martensite (observing under an optical microscope) of higher proportion on the one hand in steel, the manufacturability of product is poor on the other hand, and segregation is serious.Therefore hot rolled bainite steel rail intensity is unsuitable too high, otherwise can bring more problem to Rail Production processing and safety of railway operation.
Prior art " curve and heavy-duty steel rail bainitic steel and bainite rail and production method " thereof (CN101921971A) mainly considers that hot rolling rail is produced, do not consider the operability of accelerated cooling process condition, such as, when the element improving steel hardenability all reaches composition upper limit level, in quenching technology specification, Heating temperature and speed of cooling scope must be very narrow on the one hand, are very easy on the other hand find the serious tissues reducing steel impelling strength and fracture toughness property such as martensite under an optical microscope.Therefore the lower thermal treatment speed of cooling 10 DEG C-20 DEG C/minute of this choice of technology.
Summary of the invention
The object of the present invention is to provide a kind of high strength bainite steel rail and thermal treatment process thereof, steel grades design aspect: limit the total amount of raising hardening capacity element for finding thick M-A island tissue when checking under finding martensitic stucture or transmission electron microscope when rail after avoiding hot rolling or thermal treatment is checked under an optical microscope, the tensile strength of rail is made to be increased to more than 1400MPa by rolling postheat treatment (accelerating cooling), realize the optimum matching of intensity and toughness plasticity, make the resistance to rolling contact fatigue performance of rail and wear resistance all excellent.A small amount of multicomponent microalloying and/or thermal treatment are while significantly improving rail strength, and impelling strength, fracture toughness property also significantly improve.
The ability of alloying element conventional in steel to the hardening capacity increasing steel increases according to following order: nickel, chromium, manganese.The effect that manganese and chromium improve hardening capacity is suitable.Although the ability that nickel improves hardening capacity is lower, the toughness that steel keeps higher while improving hardening capacity, can also be made.Molybdenum can make the ferrite C curve of first analysing of bainitic steel significantly move to right, thus makes steel just all can be transformed into bainite structure under hot rolling and air cooling condition.Nickel, molybdenum due to price high, general trend adds less or do not add as far as possible, and other element is general a large amount of employing in steel.
When alloy designs, only have the less demanding steel of hardening capacity, just use single alloying element, as 40Cr, 45Mn2.Hardening capacity is required that higher steel all adopts compound aurification, unlimitedly this is because multiple element exists play complementary effect to the increase of steel hardenability simultaneously.During as nickel Individual existence, the effect increasing hardening capacity is similar to element silicon, is not outstanding, but when being added in chromium steel or chromium manganese steel by nickel, it increases the effect highly significant of hardening capacity.Therefore, at present hardening capacity is required to the formula of the chemical composition of high steel, all adopt multi-element alloyed principle, can alloys producing be given full play to so on the one hand, also can save alloy resource on the other hand.It should be noted that when employing is multi-element alloyed, note limiting the total amount improving hardening capacity element, the optimum matching of intensity and toughness plasticity could be realized like this.
The chemical composition of high strength bainite steel rail:
C：0.10％-0.32％，Si：0.80％-2.00％，Mn：0.80％-2.80％，Cr：＜1.50％，Mo：0.10％-0.40％。Wherein Mn+Cr≤2.8%, meets this requirement, can not find martensitic stucture after just guaranteeing thermal treatment under optical microphotograph.
C:0.10%-0.32%, Si:0.80%-2.00%, Mn:0.80%-2.80%, Cr:< 1.50%, wherein Mn+Cr≤2.8%.In addition compound adds Nb:0.01%-0.10%, V:0.02%-0.2%, Ti:0.005%-0.05%; Mo content is 0.10%-0.25%.
C:0.10%-0.32%, Si:0.80%-2.00%, Mn:0.80%-2.80%, Cr:< 1.50%, wherein Mn+Cr≤2.8%.In addition compound adds Nb:0.01%-0.10%, V:0.02%-0.2%, Ti:0.005%-0.05%; Do not add Mo element.
C：0.10％-0.32％，Si：0.80％-2.00％，Mn：0.80％-2.80％，Cr：＜1.50％，Mo：0.10％-0.40％；Ni：0-0.5％。Wherein Mn+Cr+0.5Ni≤2.8%, meets this requirement, can not find martensitic stucture under an optical microscope after just guaranteeing thermal treatment.
Alloys producing:
Carbon: low-carbon bainite has good toughness and weldability, carbon content too low (< 0.10%) then cannot meet the wear-resisting requirement of rail; When carbon content is too high, be unfavorable for the nucleation and growth of bainitic ferrite, the forming core of bainitic ferrite must in low-carbon (LC) district, and growing up of bainitic ferrite must spread apart as prerequisite from the Ovshinsky side of bainitic ferrite/austenite phase interface with carbon, and therefore carbon content can not higher than 0.32%.
Silicon: the formation of carbide during the special bainite transformation of prevention consumingly, impels the austenite enrichment carbon not yet changed, forms carbide-free Bainite, improve the toughness of bainitic steel.Silicone content low (< 0.80%) cannot play the effect suppressing carbide to be formed, then residual austenite content is too high for silicone content too high (> 2.00%), silicone content causes the strength degradation of steel, so should control within the scope of 0.80%-2.00%.
Nickel: the toughness that steel keeps higher can also be made while improving hardening capacity.But the more costs of its content are higher, so limit its content below 0.5%.
Manganese and chromium: manganese is similar with the effect of chromium, reduce the beginning temperature Bs that bainite is formed, and postpones and first analyse ferritic transformation, be to increase the element that cold energy power crossed by steel, be enough in lower temperature generation bainite transformation during to ensure air cooling further.Manganese, chromium content are prescribed a time limit lower than lower, do not play above-mentioned effect; Manganese element too high levels (> 2.80%), aggravate its segregation in steel, massive martensite is easily separated out in the position serious in segregation, and massive martensite can make the toughness of steel sharply reduce; Except producing martensite during chromium too high levels, also easily causing the precipitation of the carbide of chromium, reducing the toughness of steel.Because manganese and chromium are all the elements strongly improving hardening capacity, when too high levels especially Mn+Cr or Mn+Cr+0.5Ni higher than 2.8% time, when improving the hyperenergia of the hardening capacity of steel, be easy to produce a large amount of martensite, now martensite occurs with the form on lath (under opticmicroscope) or thick M-A island (under transmission electron microscope), the toughness plasticity of strong reduction steel, therefore Mn+Cr or Mn+Cr+0.5Ni should lower than 2.8%.
Carbide Nb, V, Ti: the incubation period that ferritic-pearlitic can be made to change is elongated, and the incubation period of bainite transformation shortens, bainite structure is become more readily available during air cooling, thus make steel before bainite transformation occurs, not or only have a small amount of proeutectoid ferrite to separate out, there is not perlitic transformation.
Titanium, niobium, vanadium compound add: the steel austenite Coarsening Temperature when heat containing these elements is enhanced, another even more important effect is that the carbide of these elements makes austenitic recrystallization process postpone, and therefore makes can obtain fine grained texture in the operation of rolling.
Titanium: can refinement rolling and heating time austenite crystal, and increase toughness and the rigidity of bainite structure, because remain on non-molten state in steel fusing and the titanium carbonitride of separating out when solidifying when rail reheats and is rolled.But when titanium content is less than 0.005%, this effect is just very little.On the other hand, just form the titanium carbonitride of alligatoring when titanium adds more than 0.050%, the latter just becomes the starting point of fatigue damage in operation, thus causes cracking.
Vanadium: gained in strength by the vanadium carbide nitride formed in process of cooling after precipitation-hardening hot rolling, by stoping when steel high temperature rolling the growth of crystal grain to carry out fining austenite grains, and improves the strength and stiffness of bainite structure.But when content of vanadium is less than 0.02%, this effect is just not enough.On the other hand, also above-mentioned effect can not be increased when vanadium addition is more than 0.20%.
Niobium: as vanadium, by forming niobium carbonitrides fining austenite grains.Niobium can stop Austenite Grain Growth (close to 1200 DEG C) in higher temperature region than vanadium.Niobium also improves the rigidity of bainite structure.But, these effects cannot be reached when content of niobium is less than 0.01%, and due to formation metallic compound and thick shape niobium precipitate, toughness be reduced when niobium addition level is more than 0.10%.So content of niobium will be limited between 0.01%-0.10%.
After rail hot rolling or hot rolled rail air cooling to room temperature reheat again to 850-1000 DEG C of austenitizing, after rail head of rail is cooled to 620-570 DEG C with the cooling rate of 0.3-15 DEG C/s, be chilled to 350-200 DEG C with the cooling rate of 0.5-5 DEG C/s, air cooling is to room temperature subsequently.
To 620-570 DEG C after rolling or after austenitizing, cooling rate >=0.3 DEG C/s first analyses ferritic precipitation to reduce as far as possible, cooling rate can change in a big way, be because: after rolling to process of cooling higher than bainitic transformation point temperature, can regulate according to rhythm of production and roll rear cooling rate, raising is rolled rear cooling rate and is more conducive to matching with rolling rhythm, but when rolling rear cooling rate more than 15 DEG C/more than s, the serious inequality of rail head cross-section temperature can be caused, be unfavorable for the bainite structure homogeneity produced in subsequent disposal and bainitic transformation process, easily cause section hardness uneven distribution, difficulty is brought to rail shape controlling, therefore rear cooling rate is rolled not easily more than 15 DEG C/s.Below 620-570 DEG C, be chilled to 350-200 DEG C with the cooling rate of 0.5-5 DEG C/s, the reason controlling this cooling rate is: cooling rate excessively slow (0.5 DEG C/s <), does not reach the object of build up; Cooling rate too fast (> 5 DEG C/s), then temperature homogeneity is difficult to ensure, easily causes local temperature too low, can produce the excessive martensitic stucture not wishing to obtain.Less than 350-200 DEG C air cooling to room temperature is to stop accelerating cooling more than martensitic transformation point.
For improving the stability of residual austenite, after above-mentioned accelerating cooling, air cooling need carry out temper at 250 DEG C-450 DEG C to the rail of room temperature.
The rail property of technical solution of the present invention is adopted to improve situation in table 1.
As can be seen from Table 1: after improving the element M n of hardening capacity, the raising of Cr, Ni total amount, the hardening capacity of steel improves, M-A is thicker, although tensile strength increases, but yield strength is not synchronous to be improved, and because thick M-A island is more, plasticity, the toughness of steel are all lower, obdurability coupling is poor, and now rail carries out aligning very easily rupturing.The present invention is by control Mn+Cr+0.5Ni < 2.8 or after adopting Nb, V, Ti combined microalloying, avoid in hot rolling and air cooling to granular bainite during room temperature the thick M-A island producing too much instability, so also can avoid the risk of hot rolled rail generation straightening fracture (or delayed fracture), improve the production technique adaptability of steel grade.
Table 1 adopts the rail property of technical solution of the present invention to improve situation
Restriction raising hardening capacity element total amount and/or a small amount of multicomponent microalloying rail after heat treatment tensile strength will reach more than 1400MPa, and impelling strength, fracture toughness property also significantly improve simultaneously.The wear resistance of rail generally improves along with the raising of tensile strength, therefore the resistance to rolling contact fatigue performance of bainite rail of the present invention and wear resistance all excellent.
Embodiment
The chemical composition of embodiment of the present invention bainite rail is in table 2.Embodiment of the present invention bainite rail thermal treatment process is in table 3.The mechanical property of embodiment of the present invention bainite rail is in table 4.
The composition of table 2 embodiment of the present invention rail and technique
The thermal treatment process of table 3 embodiment of the present invention rail
The mechanical property of table 4 embodiment of the present invention bainite rail
Claims (3)
1. a high strength bainite steel rail, it is characterized in that the weight percent of rail chemical composition is: C:0.18%-0.32%, Si:0.80%-2.00%, Mn:0.80%-2.00%, Cr:0.50%-1.40%, Mo:0.10%-0.40%, Ni:0-0.50%, wherein Mn+Cr+0.5Ni≤2.8%, surplus is iron and inevitable impurity.
2. a kind of high strength bainite steel rail according to claim 1, it is characterized in that described Mo:0.10%-0.25%, compound adds Nb:0.01%-0.07%, V:0.02%-0.15%, Ti:0.005%-0.050%.
3. the thermal treatment process for high strength bainite steel rail described in claim 1 or 2, after it is characterized in that rail hot rolling or hot rolled rail air cooling to room temperature reheat again to 850-1000 DEG C of austenitizing, after rail head of rail is cooled to 620-570 DEG C with the cooling rate of 0.3-15 DEG C/s, 350-200 DEG C is cooled to the cooling rate of 0.5-5 DEG C, air cooling is to room temperature subsequently, rail is heated to 250-450 DEG C again and carries out temper, air cooling is to room temperature subsequently.
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| CN102021481A (en) * | 2009-09-15 | 2011-04-20 | 鞍钢股份有限公司 | Micro-alloyed bainite steel rail and heat treatment method thereof |
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| CN102021481A (en) * | 2009-09-15 | 2011-04-20 | 鞍钢股份有限公司 | Micro-alloyed bainite steel rail and heat treatment method thereof |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN107746914A (en) * | 2017-10-16 | 2018-03-02 | 西王特钢有限公司 | A kind of U21SiMn2CrMoVRE rail new material and its heat treatment method |
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