CN1211633A - Bainitic steel rail with high-quantity binding character in its welding area - Google Patents
Bainitic steel rail with high-quantity binding character in its welding area Download PDFInfo
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Abstract
A bainitic steel rail having excellent joinability. The rail steel has a composition consisting of, by weight, 0.15-0.4% C, 0.1-0.2% Si, 0.15-1.1% Mn, <=0.035% P, <=0.035% S, 0.05-0.45% Cr, 0.005-0.15% Nb, 0.05-0.85% Mo, and the balance essentially Fe with inevitable impurities and satisfying Mn%/Si%<=5.5. In this case, a railhead has a bainitic structure, and both a railhead and railhead corners can be provided with uniform hardness distribution, and Vickers hardness is regulated to HV230 to 320.
Description
The present invention relates to be difficult in the bight of the crown in left and right sides railway rail life-span portion and head to take place the good bainitic steel rail and the manufacture method thereof of weld part connectivity of rolling contact fatigue damage and flash welding and pressure gas welding.
In the past, in rail, mainly, use perlitic steel for the wear resistance in the bight of improving crown portion and head always.But in recent years, the operational throughput that is accompanied by railway increases, and the working conditions of rail becomes increasingly serious.In Japan,, carried out annual accumulation passing tonnage being increased especially, therefore increased the generation of rail rolling contact fatigue damage in high speed that comes line and the Shinkansen and overstockedization of transportation for improving user's convenience.For this reason, each railway commercial firm is for cutting down maintenance cost, and expectation always has the abrasive rail of good anti-rolling contact fatigue.
Under existing situation, in the interval of the rolling contact fatigue damage formation problem of rail, what use is to be the common rail of the perlitic steel of 800MPa level by the normalized intensity of JIS.
On the other hand, because bainitic steel is damaging better than the anti-rolling contact fatigue of perlitic steel,, disclosed the bainitic steel rail so open in the flat 2-282448 communique for example spy.This rail has improved fatigue strength, and promotes abrasion to remove fatigue layer, to seek the abrasive raising of anti-rolling contact fatigue.
But owing to compare with the perlitic steel rail, the addition of bainitic steel rail interalloy element is many, so produce the connectivity problem of the weld part of flash welding and pressure gas welding.
Problem always in view of such the objective of the invention is to, and the connectivity and equal bainitic steel rail and the manufacture method thereof of perlitic steel rail in the past of a kind of flash welding and pressure gas welding weld part is provided
For solving above-mentioned problem, the present invention adopts the means of the following stated.
First invention is the good bainitic steel rail of weld part connectivity, it is characterized in that, contains C:0.15～0.4% in weight %, Si:0.1～0.2%, Mn:0.15～1.1% is below the P:0.035%, below the S:0.035%, Cr:0.05～0.45%, Nb:0.005～0.15%, Mo:0.05～0.85%, and satisfy Mn%/Si%≤5.5, all the other are made up of Fe and unavoidable impurities in fact
Rail's end portion is a bainite structure, and arbitrary position in the bight of rail head top and head all has the Hardness Distribution of homogeneous, and DPH is HV230～320.
Second invention is the good bainitic steel rail of weld part connectivity, it is characterized in that, in the rail steel composition of first invention, also contains Ni:0.1～1% in weight %.
The 3rd invention is the good bainitic steel rail of weld part connectivity, it is characterized in that, in the rail steel composition of first invention, also contains V:0.01～0.2% in weight %.
The 4th invention is the manufacture method of the good bainitic steel rail of weld part connectivity, it is characterized in that, possess: will have steel that the rail of first invention forms and carry out the hot rolled operation and the steel after the hot rolling are cooled to operation below 300 ℃ by the temperature more than the bainite start point with the speed of cooling of air cooling～5 ℃/second with 800～1000 ℃ of final rolling temperatures.
Fig. 1 is the cross-sectional view of rail's end portion surface location address in the expression embodiment of the present invention.
Fig. 2 represents the tensile strength of steel in the embodiment of the present invention and the relation of wear loss.
Fig. 3 represents the relation of the connectivity of the Si content of steel in the embodiment of the present invention and weld part.
Fig. 4 represents the relation of the connectivity of the Cr content of steel in the embodiments of the present invention and weld part.
Fig. 5 represents the relation of the connectivity of the Mo content of steel in the embodiments of the present invention and weld part.
Fig. 6 represents the relation of the connectivity of the Mn/Si of steel in the embodiments of the present invention and weld part.
Fig. 7 represents the relation of the connectivity of the hardness of steel in the embodiments of the present invention and weld part.
Fig. 8 represents the hardness of steel in the enforcement power formula of the present invention and the relation of wear loss ratio.
The present invention is based on the inventor and studies with keen determination the following opinion that obtains for the zygosity that improves bainitic steel rail welding section.
By to train by the time vibration, noise take some countermeasures and set out, for reducing the seam welded rails between the slit, it is very high that the frequency of use becomes, requiring has good weld part zygosity between rail. The welding method of rail has flash butt welding, gas pressure welding, pressure shaping arc welding, exothermic welding, and flash butt welding wherein and gas pressure welding are not used weld metal, is that the rail mother metal is directly engaged, thus mother metal to each other the zygosity of weld part become problem. The zygosity of the weld part of flash butt welding and gas pressure welding is subject to melt temperature, the impact of the ability of removing oxide etc. of newborn face when engaging of oxide of oxide generative capacity, the generation of composition element.
Therefore, use to have composition shown in the table 1, hardness is in the steel No.1a-1 below the DPH HV320～9,1b-1～9, and 1c-1～9,1d-1～9, the content of investigation Si, Cr, Mo and Mn/Si are on the impact of weld part zygosity.
Fig. 3～6 have shown that the content of Si, Cr, Mo and Mn/Si are on the impact of weld part zygosity.
Pole with 40 φ makes welding point through flash butt welding and gas pressure welding, the mode that becomes tension test piece parallel portion central authorities with the composition surface of joint is taked test piece, when the longitudinal axis of Fig. 3～6 represents to carry out tensile test with such test piece, the mean value (RA) of broken part section shrinkage value, the zygosity of the larger weld part of this value is higher.
Can find out that Si is 0.2%, Cr is 0.45%, Mo is 0.85%, Mn/Si surpasses at 5.5 o'clock, the section shrinkage value is below 5%, and the zygosity of weld part significantly reduces. Its reason it is believed that as described below.
Because Si, Cr are easy oxidation elements, when so its content is many, form the oxide scale film of densification on the composition surface because of the heating of flash electric current or bluster, even can not be removed by the composition surface in the final upsetting (upset) of this oxide scale film when flash butt welding or gas pressure welding, so that the zygosity of weld part reduces.
The content of Mo for a long time, the resistance to deformation height during upsetting can not fully carry out newborn face joint each other, can not get good weld part connectivity.
Therefore when the value of Mn/Si was high, the fusing point of the composite oxides of Mn, Si, Fe became remarkable high temperature, and the viscosity of the composite oxides that the junction surface is residual uprises relatively, was difficult to remove in upsetting, the connectivity of weld part was produced encumber.
Table 1
| Steel No. | Chemical ingredients (weight %) | ||||||||
| ??C | ?Si | ?Mn | ?Cr | ?Ni | ?Mo | ?Nb | ?V | ?Wn/Si | |
| ?1a-1 ?1a-2 ?1a-3 ?1a-4 ?1a-5 ?1a-6 ?1a-7 ?1a-8 ?1a-9 | ?0.28 ?0.26 ?0.31 ?0.38 ?0.29 ?0.19 ?0.29 ?0.39 ?0.15 | ?0.09 ?0.1 ?0.13 ?0.17 ?0.19 ?0.21 ?0.34 ?0.49 ?0.68 | ?0.25 ?1.09 ?0.85 ?0.34 ?0.91 ?0.64 ?0.45 ?1.03 ?0.54 | ?0.44 ?0.05 ?0.34 ?0.41 ?0.29 ?0.23 ?0.38 ?0.12 ?0.29 | ?0 ?0.12 ?0.24 ?0.25 ?0 ?0.13 ?0.34 ?0 ?0.98 | ?0.84 ?0.25 ?0.06 ?0.76 ?0.69 ?0.58 ?0.09 ?0.13 ?0.37 | ?0.12 ?0.06 ?0.009 ?0.1 ?0.06 ?0.07 ?0.05 ?0.006 ?0.14 | ?0 ?0.01 ?0.19 ?0.11 ?0.06 ?0.03 ?0.08 ?0.07 ?0 | |
| ?1b-1 ?1b-2 ?1b-3 ?1b-4 ?1b-5 ?1b-6 ?1b-7 ?1b-8 ?1b-9 | ?0.39 ?0.16 ?0.28 ?0.34 ?0.19 ?0.22 ?0.27 ?0.38 ?0.27 | ?0.13 ?0.19 ?0.17 ?0.13 ?0.11 ?0.18 ?0.15 ?0.16 ?0.12 | ?0.54 ?1.08 ?0.75 ?0.16 ?0.97 ?0.24 ?0.17 ?0.31 ?0.49 | ?0.04 ?0.06 ?0.13 ?0.31 ?0.44 ?0.48 ?0.52 ?0.68 ?0.81 | ?0 ?0 ?0.14 ?0.54 ?0 ?0.38 ?0.91 ?0.21 ?0 | ?0.76 ?0.25 ?0.46 ?0.61 ?0.11 ?0.32 ?0.18 ?0.35 ?0.84 | ?0.05 ?0.01 ?0.05 ?0.008 ?0.07 ?0.05 ?0.14 ?0.05 ?0.11 | ?0.05 ?0.13 ?0 ?0.19 ?0.01 ?0 ?0.08 ?0.09 ?0.02 | |
| ?1c-1 ?1c-2 ?1c-3 ?1c-4 ?1c-5 ?1c-6 ?1c-7 ?1c-8 ?1c-9 | 0.37 ?0.29 ?0.18 ?0.24 ?0.15 ?0.39 ?0.33 ?0.29 ?0.26 | ?0.12 ?0.19 ?0.13 ?0.15 ?0.18 ?0.11 ?0.17 ?0.14 ?0.16 | ?1.09 ?0.15 ?0.94 ?0.24 ?0.82 ?0.37 ?0.71 ?0.48 ?0.61 | ?0.05 ?0.45 ?0.12 ?0.38 ?0.25 ?0.06 ?0.43 ?0.18 ?0.31 | ?0.35 ?0.21 ?0 ?0 ?0 ?0.15 ?0.13 ?0.21 ?0.18 | ?0.04 ?0.05 ?0.13 ?0.46 ?0.72 ?0.85 ?0.91 ?1.12 ?1.57 | ?0.06 ?0.03 ?0.07 ?0.09 ?0.01 ?0.009 ?0.05 ?0.005 ?0.11 | ?0 ?0.05 ?0 ?0.05 ?0.05 ?0.02 ?0.01 ?0.03 ?0.05 | |
| ?1d-1 ?1d-2 ?1d-3 ?1d-4 ?1d-5 ?1d-6 ?1d-7 ?1d-8 ?1d-9 | ?0.24 ?0.19 ?0.33 ?0.31 ?0.24 ?0.27 ?0.29 ?0.37 ?0.15 | ?0.13 ?0.14 ?0.18 ?0.16 ?0.17 ?0.18 ?0.19 ?0.17 ?0.16 | ?0.49 ?0.62 ?0.81 ?0.77 ?0.85 ?0.98 ?1.06 ?1.01 ?1.51 | ?0.08 ?0.44 ?0.31 ?0.28 ?0.16 ?0.09 ?0.41 ?0.31 ?0.25 | ?0.35 ?0.21 ?0 ?0 ?0 ?0.15 ?0.13 ?0.21 ?0.18 | ?0.84 ?0.06 ?0.61 ?0.17 ?0.49 ?0.28 ?0.33 ?0.27 ?0.09 | ?0.06 ?0.1 ?0.07 ?0.09 ?0.009 ?0.08 ?0.007 ?0.06 ?0.14 | ?0 ?0.04 ?0 ?0.07 ?0.16 ?0.03 ?0.18 ?0.02 ?0 | ?3.77 ?4.43 ?4.50 ?4.81 ?5.00 ?5.44 ?5.58 ?5.94 ?9.44 |
One-tenth shown in the use table 2 is grouped into the steel with hardness, and investigation hardness is to the influence of weld part connectivity.
Fig. 7 shows the influence of hardness to the weld part connectivity.
Even satisfy the occasion of the scope of the invention separately at Si, Cr, Mo, Mn/Si, follow the rising of hardness, the weld part connectivity also reduces, and when particularly hardness surpassed HV320, the section shrinkage value became below 5%, becomes the problem in the practicality.
And in the occasion of any discontented unabridged version invention scope of Si, Cr, Mo, Mn/Si, even hardness below HV320, the weld part connectivity also reduces.
Table 2
| Steel No. | Chemical ingredients (weight %) | Hardness HV | ||||||||
| ?C | ?Si | ?Mn | ?Cr | ????Ni | ?Mo | ?Nb | ?V | ?Wn/Si | ||
| ????1 ????2 ????3 ????4 ????5 ????6 ????7 ????8 ????9 ????10 ????11 ????12 ????13 ????14 | ?0.28 ?0.40 ?0.37 ?0.31 ?0.33 ?0.22 ?0.19 ?0.39 ?0.37 ?0.38 ?0.31 ?0.33 ?0.38 ?0.33 | ?0.19 ?0.12 ?0.17 ?0.16 ?0.18 ?0.16 ?0.18 ?0.14 ?0.11 ?0.13 ?0.19 ?0.18 ?0.16 ?0.18 | ?0.85 ?0.45 ?0.91 ?0.84 ?0.85 ?0.76 ?0.84 ?0.65 ?0.45 ?0.48 ?0.84 ?0.75 ?0.88 ?0.76 | ?0.43 ?0.31 ?0.42 ?0.38 ?0.41 ?0.16 ?0.17 ?0.44 ?0.37 ?0.44 ?0.19 ?0.34 ?0.44 ?0.39 | ????0.1 ????0.19 ????0.6 ????0.2 ????0 ????0 ????0 ????0.8 ????0 ????0 ????0 ????0 ????0.8 ????0 | ?0.55 ?0.43 ?0.31 ?0.49 ?0.28 ?0.79 ?0.81 ?0.34 ?0.79 ?0.85 ?0.79 ?0.76 ?0.55 ?0.84 | ?0.05 ?0.15 ?0.09 ?0.08 ?0.08 ?0.09 ?0.15 ?0.14 ?0.08 ?0.13 ?0.14 ?0.12 ?0.11 ?0.14 | ?0.05 ?019 ?0.05 ?0.09 ?0.19 ?0.17 ?0.09 ?0.19 ?0.17 ?0.07 ?0.17 ?0.18 ?0.19 ?0.19 | ?4.47 ?3.75 ?5.35 ?5.25 ?4.72 ?4.75 ?4.67 ?4.64 ?4.09 ?3.69 ?4.42 ?4.17 ?5.50 ?4.22 | ?234 ?239 ?242 ?244 ?245 ?249 ?254 ?267 ?280 ?299 ?320 ?323 ?336 ?357 |
Thereby, in order to ensure sufficient weld part connectivity, Si must be decided to be below 0.2%, Cr is decided to be below 0.45%, Mo is decided to be below 0.85%, Mn/Si is decided to be below 5.5, again hardness is decided to be below the HV320.
Below, the qualification reason that the present invention beyond above-mentioned is constituted main points describes.
(1) composition compositing range
C:C is for guaranteeing the essential element of intensity, when less than 0.15%, is difficult to guarantee at an easy rate the hardness as rail.And surpass at 0.4% o'clock, easily generate the martensite that head is become fragile.Thereby with its content tailor-made 0.15～0.4%.
Si:Si is not only effective as reductor, also is the element that intensity is risen, but does not see its effect during less than 0.1%.Its upper limit is 0.2% as mentioned above.Thereby with its content tailor-made 0.1～0.2%.
Mn:Mn reduces the bainite transformation temperature hardening capacity is improved, and takes this to invest the element of rail high strength.But its effect is little during less than 0.15%, and the microsegregation that surpasses 1.1% o'clock invar easily generates martensite, because of sclerosis and embrittlement the material deterioration takes place when thermal treatment and during welding.Thereby with its content tailor-made 0.15～1.1%.
P: the excessive P of containing makes the toughness deterioration of steel, and is therefore tailor-made below 0.035%.
S:S is present in the steel as main inclusion, but surpasses at 0.035% o'clock, and this inclusion amount significantly increases, and causes the material deterioration that embrittlement causes, and is therefore tailor-made below 0.035%.
Cr:Cr is the element that promotes bainite transformation, is to make to resemble the rail of the present invention the important element that microstructure is become for bainite structure.It is little to change facilitation effect during less than 0.05%, and microstructure can not become the bainite structure of homogeneous.Its upper limit such as above-mentioned be 0.45%.Thereby to get its content be 0.05～0.45%.
Mo:Mo is the element that promotes bainite transformation, is to make to resemble the rail of the present invention the important element that microstructure is become for bainite structure.It is low to change facilitation effect during less than 0.05%, and microstructure can not become the bainite structure of homogeneous.Its upper limit such as above-mentioned be 0.85%.Thereby to get its content be 0.05～0.85%.
Nb:Nb not only promotes bainite transformation, and is combined in and separates out after rolling with C in the steel, is consolidated to the inside of rail's end portion, and wear resistant is improved, and prolongs the life-span of rail.This effect is little during less than 0.005%, and it is saturated to surpass 0.15% o'clock this effect, thereby its content is taken as 0.005～0.15%.
In the present invention, except that above-mentioned composition element,, preferably contain Ni or V again for improving intensity, the wear resistant of steel.At this moment,
Ni:Ni promotes bainite transformation, for the high strength effective elements, but does not see its effect during less than 0.1%, and it is saturated to surpass 1% o'clock its effect, therefore its content is taken as 0.1～1%.
V:V and Nb are same, are combined in C in the steel and separate out after rolling, prolong the life-span of rail, but its effect is little during less than 0.01%, and it is saturated to surpass 0.2% o'clock its effect, therefore its content is taken as 0.01～0.2%.
(2) metal structure
Bainite structure and pearlitic structure are in the past compared, and when comparing under same tensile strength, to improving fatigue strength, it is effective prolonging rolling fatigue life.And as shown in Figure 2, wear loss is many to be effectively to removing fatigue layer, and therefore rail's end portion must be a bainite structure at least.
(3) hardness (wear resistant)
About wear loss, wish most to estimate, but the method for using western former formula wear testing machine to estimate also is effective with the wear loss of laying on the spot.Use this test method(s) the short period of time wear resistant (relation of hardness and wear loss ratio) to be estimated.
The steel that alloying element content is done various variations as shown in table 3 is added to 1250 ℃, in 920 ℃ rolling after, air cooling is made test portion.Get the western former formula abrasion test piece of external diameter 30mm, wide 8mm then by test portion, under contact loading 130kg, sliding ratio-10%, unlubricated dose condition, carry out wear test, measure the wear loss after the revolution 500,000 times.Estimate according to following method: the wear loss by JIS measures the common rail of perlitic steel of normalized HV280 degree, adopt the ratio with respect to the test portion wear loss of the common rail of perlitic steel.
Table 3
| Steel No. | Chemical ingredients (weight %) | Hardness HV | |||||||
| ??C | ??Si | ?Mn | ?Cr | ?Ni | ?Mo | ?Nb | ?V | ||
| ?1 ?2 ?3 ?4 ?5 ?6 ?7 ?8 ?9 | ?0.25 ?0.34 ?0.39 ?0.29 ?0.38 ?0.4 ?0.31 ?0.39 ?0.37 | ?0.1 ?0.12 ?0.18 ?0.14 ?0.17 ?0.13 ?0.19 ?0.11 ?0.15 | ?0.45 ?0.64 ?0.99 ?0.76 ?0.91 ?0.71 ?1.04 ?0.57 ?0.75 | ?0.29 ?0.34 ?0.39 ?0.44 ?0.29 ?0.37 ?0.43 ?0.41 ?0.45 | ?0.2 ?0.13 ?0 ?0.3 ?0.2 ?0.4 ?0 ?0 ?0 | ?0.81 ?0.49 ?0.37 ?0.64 ?0.59 ?0.64 ?0.77 ?0.75 ?0.85 | ?0.05 ?0.13 ?0.005 ?0.07 ?0.01 ?0.05 ?0.04 ?0.15 ?0.11 | ?0.01 ?0.08 ????0 ?0.04 ?0.08 ?0.12 ?0.05 ?0.18 ?0.19 | ?171 ?227 ?232 ?243 ?268 ?284 ?319 ?330 ?370 |
Fig. 8 shows the influence of hardness to the wear loss ratio.
Under same hardness, to compare with pearlitic structure, the wear loss of bainite structure demonstrates about 2 times value than big.During HV less than 230, the wearing and tearing decrement is than surpassing 3 times, and compares based on the rail replacement life-span of accumulative total passing tonnage, and the replacing life-span of hanking because of abrasion significantly shortens, and the problem in the practicality takes place.Thereby the lower value of hardness got make HV230.Be limited to HV320 on it, in order that do not cause the reduction of weld part connectivity as mentioned above.Thereby, the arbitrary position in the crown of head shown in Figure 1 portion 1, head bight 2, the also tailor-made HV230 of DPH～320.
For crown portion, head bight, try to carry out to change hardness by intention, as method to controlling with the contact condition of wheel, but in actual path, the contact condition of rail and wheel is often to change, and the Hardness Control contact condition that change head is actually difficulty to prolong rail life.Thereby crown portion, any position, head bight all must take the Hardness Distribution of homogeneous.All apply the thermal treatment of similarity condition by correct top and head bight, obtain the Hardness Distribution of such homogeneous.
As discussed above, by being adjusted to the scope of being grouped into, metal structure and hardness, just can obtain the weld part connectivity and the equal bainitic steel rail of perlitic steel rail in the past of flash welding and pressure gas welding.
The rail that can have such characteristic according to following manufacture method manufacturing.
(4) rail manufacturing method
To have the present invention and become the steel be grouped into, carry out hot rolling for 800～1000 ℃,, be cooled to below 300 ℃ with the speed of cooling of air cooling～5 ℃/second then by the temperature more than the bainite start point with final rolling temperature.
A. final rolling temperature: 800 ℃ of final rolling temperature less thaies are below it the time, and the beginning ferritic transformation reduces intensity.And finishing temperature is when surpassing 1000 ℃, and remarkable thickization of the bainite structure after the hot rolling makes and guarantee the toughness difficulty.Thereby, with tailor-made 800～1000 ℃ of final rolling temperature.
B. speed of cooling: have the steel that the present invention becomes to be grouped into,, can guarantee desirable intensity, toughness even air cooling also obtains bainite structure.But, when speed of cooling surpasses 5 ℃/second, generate martensite, toughness is significantly reduced.Thereby with the tailor-made air cooling of speed of cooling～5 ℃/second.
Embodiment
The steel (steel of the present invention: NO.2～4, comparative steel: NO.1,5,6) that will have composition shown in the table 4 is heated to 1250 ℃, 920 ℃ rolling after, use the steel plate of the thickness of slab 12mm behind the air cooling, carry out measurement of hardness, wear test, the evaluation test of weld part connectivity.About wear test, get the test piece of external diameter 30mm, wide 8mm by rolled sheet material, take the rim test piece of same size by the railway wheel material, use western former formula wear testing machine, under sliding ratio-10%, contact loading 130kg, unlubricated dose condition, they are tested, measure the wear loss after the revolution 500,000 times, take and the ratio of the wear loss of the rail of the HV275 pearlitic structure of usefulness as a comparison, obtain the wear loss ratio.
With hardness, wear loss the table 5 that the results are shown in than, connectivity.
Than the low comparative steel No.1 of steel C amount of the present invention, hardness is 221, the lower value of the not enough scope of the invention, and wear loss compares also up to 3.21, thereby is unsuitable for practicality.And than the high comparative steel No.5 of steel C amount of the present invention, 6, microstructure is a pearlitic structure, so wear characteristic is good, but anti-rolling contact fatigue is damaging poor.
In contrast, composition satisfies the steel No.2 of the present invention of the scope of the invention, and 3,4, hardness is in the scope of the invention of HV230～320, and wear loss is than the optimum range that also is in 1.3～3.And the weld part connectivity is because Mn/Si is 5.5 below, HV is also below 320, so demonstrate the high value.
Table 4
| Steel No. | Chemical ingredients (weight %) | Appendix | ||||||||
| ?C | ?Si | ?Mn | ?Cr | ?Ni | ?Mo | ?Nb | ?V | Mn/Si | ||
| ????1 | ?0.14 * | ?0.19 | ?1.04 | ?0.44 | ?0 | ?0.54 | ?0.05 | ?0.09 | ?5.47 | Comparative steel |
| ????2 | ?0.25 | ?0.18 | ?0.95 | ?0.34 | ?0 | ?0.8 | ?0.09 | ?0.01 | ?5.28 | Steel of the present invention |
| ????3 | ?0.31 | ?0.18 | ?0.88 | ?0.16 | ?0 | ?0.75 | ?0.09 | ?0.13 | ?4.89 | Steel of the present invention |
| ????4 | ?0.39 | ?0.15 | ?0.75 | ?0.28 | ?0 | ?0.5 | ?0.07 | ?0.09 | ?5.00 | Steel of the present invention |
| ????5 | ?0.49 * | ?0.12 | ?0.64 | ?0.38 | ?0 | ?0.11 | ?0.15 | ?0.19 | ?5.33 | Comparative steel |
| ????6 | ?0.52 * | ?0.14 | ?0.74 | ?0.42 | ?0 | ?0.21 | ?0.05 | ?0.18 | ?5.29 | Comparative steel |
Annotate)
*Number be illustrated in outside the scope of the present invention.
Table 5
| Steel No. | Hardness HV | The wear loss ratio | Connectivity RA (%) | Microstructure | Appendix |
| ????1 | ????221 * | ????3.21 * | ????35 | Bainite | Comparative steel |
| ????2 | ????277 | ????1.8 | ????28 | Bainite | Steel of the present invention |
| ????3 | ????288 | ????1.5 | ????25 | Bainite | Steel of the present invention |
| ????4 | ????245 | ????2.8 | ????30 | Bainite | Steel of the present invention |
| ????5 | ????253 | ????1.05 * | ????15 | Bainite | Comparative steel |
| ????6 | ????275 | ????1 * | ????20 | Bainite | Comparative steel |
Annotate)
*Number be illustrated in outside the scope of the present invention.
The steel (steel of the present invention: No.2～6,9,10,13, comparative steel: No.1,7,8,11,12,14) that use has composition shown in the table 6 carries out test similarly to Example 1.
With hardness, wear loss the table 7 that the results are shown in than, weld part connectivity.
Steel all has bainite structure.The comparative steel No.1 that the content of Mn, Cr, Mo is lower than the present invention steel, 8,12, though the weld part connectivity is high, hardness is low, the wear loss ratio is respectively up to 3.15,3.45,3.22.
In addition, the comparative steel No.7,11,14 that the content of Mn, Cr, Mo is higher than the present invention steel, the wear loss ratio is below 1.3.And the weld part connectivity also is reduced to below 5%.
In contrast, steel No.2 of the present invention～6,9,10,13, its hardness, wear loss ratio, weld part connectivity all demonstrate good value.
Table 6
| Steel No. | Chemical ingredients (weight %) | Appendix | ||||||||
| ?C | ?Si | ?Mn | ?Cr | ?Ni | ?Mo | ?Nb | ?V | Mn/Si | ||
| ????1 | ?0.38 | ?0.2 | ?0.14 * | 0.13 | ?0.2 | ?0.84 | ?0.14 | ?0.13 | ?0.70 | Comparative steel |
| ????2 | ?0.27 | ?0.18 | ?0.97 | ?0.35 | ?0.13 | ?0.8 | ?0.07 | ?0.09 | ?5.39 | Steel of the present invention |
| ????3 | ?0.31 | ?0.11 | ?0.6 | ?0.19 | ????0 | ?0.79 | ?0.09 | ?0.08 | ?5.45 | Steel of the present invention |
| ????4 | ?0.35 | ?0.16 | ?0.84 | ?0.34 | ?0.3 | ?0.5 | ?0.07 | ?0.11 | ?5.25 | Steel of the present invention |
| ????5 | ?0.37 | ?0.19 | ?1.04 | ?0.29 | ?0.2 | ?0.11 | ?0.12 | ?0.16 | ?5.47 | Steel of the present invention |
| ????6 | ?0.39 | ?0.17 | ?0.93 | ?0.19 | ?0.4 | ?0.33 | ?0.05 | ?0.19 | ?5.47 | Steel of the present invention |
| ????7 | ?0.25 | ?0.18 | ?1.65 * | 0.05 | ?0.2 | ?0.49 | ?0.05 | ?0.18 | ?9.17 * | Comparative steel |
| ????8 | ?0.27 | ?0.15 | ?0.82 | ?0.04 * | ?0.13 | ?0.5 | ?0.15 | ?0.15 | ?5.47 | Comparative steel |
| ????9 | ?0.31 | ?0.16 | ?0.86 | ?0.37 | ????0 | ?0.64 | ?0.09 | ?0.02 | ?5.38 | Steel of the present invention |
| ???10 | ?0.35 | ?0.12 | ?0.57 | ?0.41 | ?0.3 | ?0.5 | ?0.07 | ?0.19 | ?4.75 | Steel of the present invention |
| ???11 | ?0.37 | ?0.17 | ?0.55 | ?0.55 * | ?0.2 | ?0.83 | ?0.13 | ?0.09 | ?3.24 | Comparative steel |
| ???12 | ?0.39 | ?0.19 | ?0.75 | ?0.44 | ?0.4 | ?0.04 * | 0.15 | ?0.17 | ?3.95 | Comparative steel |
| ???13 | ?0.25 | ?0.13 | ?0.71 | ?0.41 | ?0.2 | ?0.55 | ?0.12 | ?0.16 | ?5.46 | Steel of the present invention |
| ???14 | ?0.31 | ?0.16 | ?0.88 | ?0.29 | ?0.4 | ?0.95 * | 0.05 | ?0.11 | ?5.50 | Comparative steel |
Annotate)
*Number be illustrated in outside the scope of the present invention.
Table 7
| Steel No. | Hardness HV | The wear loss ratio | Connectivity RA (%) | Microstructure | Appendix |
| ????1 | ????221 * | ????3.15 * | ????35 | Bainite | Comparative steel |
| ????2 | ????306 | ????1.35 | ????28 | Bainite | Steel of the present invention |
| ????3 | ????234 | ????2.85 | ????25 | Bainite | Steel of the present invention |
| ????4 | ????259 | ????2.25 | ????30 | Bainite | Steel of the present invention |
| ????5 | ????247 | ????2.31 | ????25 | Bainite | Steel of the present invention |
| ????6 | ????252 | ????2.29 | ????20 | Bainite | Steel of the present invention |
| ????7 | ????328 * | ????0.89 * | ????4 * | Bainite | Comparative steel |
| ????8 | ????217 * | ????3.45 * | ????28 | Bainite | Comparative steel |
| ????9 | ????260 | ????2.23 | ????25 | Bainite | Steel of the present invention |
| ????10 | ????243 | ????2.81 | ????30 | Bainite | Steel of the present invention |
| ????11 | ????326 * | ????0.93 * | ????4 * | Bainite | Comparative steel |
| ????12 | ????225 * | ????3.22 * | ????20 | Bainite | Comparative steel |
| ????13 | ????244 | ????2.88 | ????24 | Bainite | Steel of the present invention |
| ????14 | ????326 * | ????0.9 * | ????4 * | Bainite | Comparative steel |
Annotate)
*Number be illustrated in outside the scope of the present invention.
The steel (steel of the present invention: No.1,3,4,7,10, comparative steel: No.2,5,6,8,9,11) that use has composition shown in the table 8 carries out test similarly to Example 1.
With hardness, wear loss the table 9 that the results are shown in than, weld part connectivity.
Steel all has bainite structure.Steel No.1 of the present invention does not contain Ni, V, but hardness is in the scope of the invention, and wear loss when weld part connectivity all demonstrates suitable value.
Ni, the comparative steel No.2 that V content is lower than the scope of the invention, 6,8, to compare with the steel No.1 of the present invention that does not contain Ni, V, hardness, wear loss ratio, weld part connectivity all change hardly, find to contain the effect of Ni, V.
Ni content satisfies the steel No.3 of the present invention of the scope of the invention, and 4,7, hardness is in the scope of the invention, and wear loss when weld part connectivity all demonstrates suitable value, and steel No.1 of the present invention has better value.Ni content surpasses the comparative steel No.5 of steel of the present invention, and 9, true hardness, wear loss ratio, weld part connectivity and steel No.4 of the present invention, 7 is equal, and it is saturated to contain the Ni effect.
V content satisfies the steel No.10 of the scope of the invention, and hardness is in the scope of the invention, and wear loss when weld part connectivity all demonstrates suitable value, and steel No.1 of the present invention has better value.V content surpasses the comparative steel No.11 of the scope of the invention, and the connectivity and the steel No.10 of the present invention of its hardness, wear loss ratio, weld part are equal, and it is saturated to contain the V effect.
Table 8
| Steel No. | Chemical ingredients (weight %) | Appendix | ||||||||
| ??C | ??Si | ??Mn | ??Cr | ?Ni | ?Mo | ?Nb | ????V | Mn/Si | ||
| 1 | ?0.31 | ?0.19 | ?1.04 | ?0.37 | ?0 | 0.67 | ?0.01 | ????0 | ?5.47 | Steel of the present invention |
| 2 | ?0.31 | ?0.19 | ?1.04 | ?0.37 | ?0.09 * | 0.67 | ?0.01 | ????0 | ?5.47 | Comparative steel |
| 3 | ?0.37 | ?0.13 | ?0.71 | ?0.44 | ?0.21 | ?0.45 | ?0.13 | ????0 | ?5.46 | Steel of the present invention |
| 4 | ?0.27 | ?0.17 | ?0.93 | ?0.33 | ?0 | ?0.79 | ?0.02 | ????0 | ?5.47 | Steel of the present invention |
| 5 | ?0.27 | ?0.17 | ?0.93 | ?0.33 | ?1.1 * | ?0.79 | ?0.02 | ????0 | ?5.47 | Comparative steel |
| 6 | ?0.31 | ?0.19 | ?1.04 | ?0.37 | ?0 | ?0.67 | ?0.01 | ?0.007 * | ?5.47 | Comparative steel |
| 7 | ?0.33 | ?0.19 | ?1.02 | ?0.33 | ?0.3 | ?0.67 | ?0.009 | ?0.08 | ?5.37 | Steel of the present invention |
| 8 | ?0.31 | ?0.19 | ?1.04 | ?0.37 | ?0.08 * | 0.67 | ?0.01 | ?0.007 * | ?5.47 | Comparative steel |
| 9 | ?0.33 | ?0.19 | ?1.02 | ?0.33 | ?1.5 * | 0.67 | ?0.009 | ?0.08 | ?5.37 | Comparative steel |
| 10 | ?0.27 | ?0.17 | ?0.92 | ?0.38 | ?0 | ?0.61 | ?0.03 | ?0.13 | ?5.41 | Steel of the present invention |
| 11 | ?0.27 | ?0.17 | ?0.92 | ?0.38 | ?0 | ?0.61 | ?0.03 | ?0.21 * | 5.41 | Comparative steel |
Annotate)
*Number be illustrated in outside the scope of the present invention.
Table 9
| Steel No. | Hardness HV | The wear loss ratio | Connectivity RA (%) | Microstructure | Appendix |
| ????1 | ?268 | ????2.21 | ????30 | Bainite | Steel of the present invention |
| ????2 | ?268 | ????2.21 | ????32 | Bainite | Comparative steel |
| ????3 | ?235 | ????2.86 | ????25 | Bainite | Steel of the present invention |
| ????4 | ?254 | ????2.24 | ????30 | Bainite | Steel of the present invention |
| ????5 | ?254 | ????2.24 | ????25 | Bainite | Comparative steel |
| ????6 | ?268 | ????2.2 | ????37 | Bainite | Comparative steel |
| ????7 | ?289 | ????2.08 | ????35 | Bainite | Steel of the present invention |
| ????8 | ?268 | ????2.2 | ????39 | Bainite | Comparative steel |
| ????9 | ?289 | ????2.08 | ????25 | Bainite | Comparative steel |
| ????10 | ?262 | ????2.23 | ????32 | Bainite | Steel of the present invention |
| ????11 | ?262 | ????2.23 | ????31 | Bainite | Comparative steel |
Embodiment 4
The steel (steel of the present invention: No.2,3,5,6, comparative steel: No.1,4,7,8) that use has table 10 expression composition carries out test similarly to Example 1.
Hardness, wear loss ratio, weld part connectivity are shown in table 11.
Steel all has bainite structure.The content of Si, Cr, Mo is in the scope of the present invention, and Mn/Si is the steel No.2 of the present invention below 5.5, and 3,5,6, hardness, wear loss all demonstrate good value than, weld part connectivity.
But, satisfying the occasion of the scope of the invention separately at Si, Cr, Mo content, Mn/Si surpasses 5.5 comparative steel No.1, and 4, the connectivity of weld part is poor.On the other hand, Mn/Si satisfies the occasion below 5.5, and the independent content of Si surpasses the comparative steel No.7 of the scope of the invention, and 8, the connectivity of same weld part is poor.
Table 10
| Steel No. | Chemical ingredients (weight %) | Appendix | ||||||||
| C | ?Si | ??Mn | ?Cr | ??Ni | ?Mo | ?Nb | ???V | ?Mn/S ??i | ||
| ????1 | ?0.31 | ?0.18 | ?1.35 * | ?0.39 | ?0.15 | ?0.3.1 | ?0.03 | ?0 | ?7.50 * | Comparative steel |
| ????2 | ?0.25 | ?0.16 | ?0.85 | ?0.45 | ?0 | ?0.81 | ?0.02 | ?0.05 | ?5.31 | Steel of the present invention |
| ????3 | ?0.37 | ?0.17 | ?0.93 | ?0.41 | ?0.11 | ?0.49 | ?0.06 | ?0 | ?5.47 | Steel of the present invention |
| ????4 | ?0.27 | ?0.13 | ?1.15 * | ?0.25 | ?0 | ?0.45 | ?0.05 | ?0.11 | ?8.85 * | Comparative steel |
| ????5 | ?0.35 | ?0.15 | ?0.64 | ?0.31 | ?0.32 | ?0.76 | ?0.07 | ?0 | ?4.27 | Steel of the present invention |
| ????6 | ?0.31 | ?0.19 | ?0.79 | ?0.35 | ?0 | ?0.35 | ?0.11 | ?0.19 | ?4.16 | Steel of the present invention |
| ????7 | ?0.33 | ?0.22 * | ?1.04 | ?0.28 | ?0.18 | ?0.51 | ?0.12 | ?0 | ?4.73 | Comparative steel |
| ????8 | ?0.31 | ?0.31 * | ?0.99 | ?0.27 | ?0 | ?0.67 | ?0.09 | ?0.09 | ?3.19 | Comparative steel |
Annotate)
*Number be illustrated in outside the scope of the present invention.
Table 11
| Steel No. | Hardness HV | The wear loss ratio | Connectivity RA (%) | Microstructure | Appendix |
| ????1 | ????257 | ????2.21 | ????4 * | Bainite | Comparative steel |
| ????2 | ????266 | ????2.18 | ????32 | Bainite | Steel of the present invention |
| ????3 | ????257 | ????2.21 | ????25 | Bainite | Steel of the present invention |
| ????4 | ????249 | ????2.45 | ????3 * | Bainite | Comparative steel |
| ????5 | ????242 | ????2.48 | ????25 | Bainite | Steel of the present invention |
| ????6 | ????242 | ????2.49 | ????37 | Bainite | Steel of the present invention |
| ????7 | ????267 | ????2.19 | ????3 * | Bainite | Comparative steel |
| ????8 | ????302 | ????1.89 | ????4 * | Bainite | Comparative steel |
Annotate)
*Number be illustrated in outside the scope of the present invention.
Use the steel No.1 shown in the table 12,2, make final rolling temperature 760～1030 ℃ range, be rolled into actual rail shape, make the range of speed of cooling in air cooling～6.5 ℃/second then.Then, the result of the hardness of the rail of inquiry agency one-tenth, wear loss ratio, connectivity.Wherein, wear loss is taken from the wear test of rolled stock head shown in embodiment 1 sample than taking, and estimates by test method(s) similarly to Example 1.
Show the result in table 13 (example of the present invention: No.2～6,8～10,12, comparative example: No.1,7,11,13).
Comparative example No.1, speed of cooling satisfies condition of the present invention, does not satisfy final rolling temperature, therefore though the connectivity of weld part is good, but HV220, wear loss than 3.11, wear characteristic is poor.
Final rolling temperature, speed of cooling are satisfied in the present invention's example No.2～6,8～10,12, therefore demonstrate HV230～320, wear loss than 1.3～3 good values, and connectivity are also good.
Comparative example No.7,11, final rolling temperature satisfies condition, but speed of cooling is too fast, so hardness surpasses HV320, wear characteristic, weld part connectivity deterioration.
Comparative example No.13, the final rolling temperature height is organized thickly, so hardening capacity uprises, HV surpasses 320.
Table 12
| Steel No. | Chemical ingredients (weight %) | Hardness HV | Appendix | ||||||||
| C | ?Si | ?Mn | ?Cr | ?Ni | ?Mo | ?Nb | ?V | ?Mn/ | |||
| 1 | ?0.29 | ?0.18 | ?0.95 | ?0.29 | ?0 | ?0.69 | ?0.05 | ?0.05 | ?5.28 | ?263 | Steel of the |
| 2 | ?0.33 | ?0.16 | ?0.45 | ?0.45 | ?0.1 | ?0.85 | ?0.09 | ?0.11 | ?2.81 | ?276 | Steel of the present invention |
Table 13
| Condition No. | Steel No. | Final rolling temperature (℃) | Speed of cooling (℃/second) | Hardness HV | The wear loss ratio | Connectivity RA (%) | Appendix |
| 1 | ?1 | ?760 * | ????0.5 | ?220 * | ????3.11 * | ????31 | Comparative example |
| 2 | ?2 | ?810 | ????2.6 | ?311 | ????1.35 | ????27 | Example of the present invention |
| 3 | ?1 | ?820 | ????1.7 | ?237 | ????2.84 | ????32 | Example of the present invention |
| 4 | ?2 | ?845 | ????2.5 | ?289 | ????2.25 | ????27 | Example of the present invention |
| 5 | ?1 | ?850 | ????1.1 | ?275 | ????2.37 | ????31 | Example of the present invention |
| 6 | ?2 | ?867 | ????0.8 | ?255 | ????2.46 | ????28 | Example of the present invention |
| 7 | ?1 | ?870 | ????5.7 * | ?345 * | ????1.12 * | ????5 | Comparative example |
| 8 | ?2 | ?885 | ????0.4 | ?248 | ????2.58 | ????31 | Example of the present invention |
| 9 | ?1 | ?910 | ????1.1 | ?267 | ????2.41 | ????26 | Example of the present invention |
| 10 | ?2 | ?935 | ????1.8 | ?273 | ????2.34 | ????21 | Example of the present invention |
| 11 | ?1 | ?955 | ????6.5 * | ?415 * | ????0.91 * | ????4 * | Comparative example |
| 12 | ?2 | ?985 | ????2.4 | ?286 | ????2.28 | ????21 | Example of the present invention |
| 13 | ?1 | ?1030 * | ????1.2 | ?342 * | ????1.13 * | ????5 | Comparative example |
Annotate)
*Number be illustrated in outside the scope of the present invention.
Claims (4)
1. the bainitic steel rail that the weld part connectivity is good is characterized in that, contains C:0.15～0.4% in weight %, Si:0.1～0.2%, Mn:0.15～1.1% is below the P:0.035%, below the S:0.035%, Cr:0.05～0.45%, Nb:0.005～0.15%, Mo:0.05～0.85%, and satisfy Mn%/Si%≤5.5, all the other are made up of Fe and unavoidable impurities in fact
Rail's end portion is a bainite structure, and arbitrary position in rail head top and head bight all has the Hardness Distribution of homogeneous, and DPH is HV230～320.
2. the good bainitic steel rail of the described weld part connectivity of claim 1 is characterized in that, as composition of steel, also contains Ni:0.1～1% in weight %.
3. the good bainitic steel rail of the described weld part connectivity of claim 1 is characterized in that, as composition of steel, also contains V:0.01～0.2% in weight %.
4. the manufacture method of the bainitic steel rail that the weld part connectivity is good is characterized in that possessing: the steel that will have a described composition of claim 1 with 800～1000 ℃ of final rolling temperatures carry out the hot rolled operation and
Steel after the hot rolling by the temperature more than the bainite start point, are cooled to operation below 300 ℃ with the speed of cooling of air cooling～5 ℃/second.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP250534/1997 | 1997-09-16 | ||
| JP25053497A JP3649872B2 (en) | 1997-09-16 | 1997-09-16 | Bainite steel rail with excellent weldability |
| JP250534/97 | 1997-09-16 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1211633A true CN1211633A (en) | 1999-03-24 |
| CN1074058C CN1074058C (en) | 2001-10-31 |
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Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN98102489A Expired - Fee Related CN1074058C (en) | 1997-09-16 | 1998-05-07 | Bainitic steel rail with high-quantity binding character in its welding area |
Country Status (2)
| Country | Link |
|---|---|
| JP (1) | JP3649872B2 (en) |
| CN (1) | CN1074058C (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102534403A (en) * | 2010-12-17 | 2012-07-04 | 鞍钢股份有限公司 | Bainite heat-treated steel rail and heat treatment method thereof |
| CN102534387A (en) * | 2011-12-12 | 2012-07-04 | 中国铁道科学研究院金属及化学研究所 | Bainite/martensite steel rail with 1,500 Mpa level of high toughness and manufacturing method thereof |
| CN103409693A (en) * | 2013-07-31 | 2013-11-27 | 内蒙古包钢钢联股份有限公司 | Steel used for bainite rail, and manufacturing method thereof |
| CN108385022A (en) * | 2018-03-30 | 2018-08-10 | 鞍钢股份有限公司 | High-strength, high-toughness, wear-resistant and corrosion-resistant bainite steel rail for heavy-duty railway and manufacturing method thereof |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2840628B1 (en) | 2002-06-05 | 2004-08-13 | Cogifer | RAIL TRACK COMPRISING A TRACK APPARATUS ELEMENT AND A WELDED RAIL SECTION WITHOUT MATERIAL SUPPLY |
| CN101921971B (en) * | 2010-09-08 | 2013-03-13 | 北京特冶工贸有限责任公司 | Bainite steel and bainite steel rail used for curve and heavy load steel rail, and production method thereof |
| CN102936700B (en) * | 2012-10-30 | 2014-07-23 | 燕山大学 | Full bainitic steel frog and manufacturing method thereof |
| CN104152805A (en) * | 2014-07-25 | 2014-11-19 | 安徽霍山科皖特种铸造有限责任公司 | Alloy steel and thermal treatment method thereof |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2620369B2 (en) * | 1989-04-20 | 1997-06-11 | 新日本製鐵株式会社 | Rails with excellent rolling fatigue resistance |
-
1997
- 1997-09-16 JP JP25053497A patent/JP3649872B2/en not_active Expired - Lifetime
-
1998
- 1998-05-07 CN CN98102489A patent/CN1074058C/en not_active Expired - Fee Related
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102534403A (en) * | 2010-12-17 | 2012-07-04 | 鞍钢股份有限公司 | Bainite heat-treated steel rail and heat treatment method thereof |
| CN102534387A (en) * | 2011-12-12 | 2012-07-04 | 中国铁道科学研究院金属及化学研究所 | Bainite/martensite steel rail with 1,500 Mpa level of high toughness and manufacturing method thereof |
| CN103409693A (en) * | 2013-07-31 | 2013-11-27 | 内蒙古包钢钢联股份有限公司 | Steel used for bainite rail, and manufacturing method thereof |
| CN108385022A (en) * | 2018-03-30 | 2018-08-10 | 鞍钢股份有限公司 | High-strength, high-toughness, wear-resistant and corrosion-resistant bainite steel rail for heavy-duty railway and manufacturing method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN1074058C (en) | 2001-10-31 |
| JPH1192866A (en) | 1999-04-06 |
| JP3649872B2 (en) | 2005-05-18 |
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