WO2018010494A1 - 一种过共析钢轨及其制备方法 - Google Patents
一种过共析钢轨及其制备方法 Download PDFInfo
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- WO2018010494A1 WO2018010494A1 PCT/CN2017/085651 CN2017085651W WO2018010494A1 WO 2018010494 A1 WO2018010494 A1 WO 2018010494A1 CN 2017085651 W CN2017085651 W CN 2017085651W WO 2018010494 A1 WO2018010494 A1 WO 2018010494A1
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/04—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rails
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/003—Cementite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/009—Pearlite
Definitions
- the invention relates to the field of railways, and in particular to a hypereutectoid steel rail and a preparation method thereof.
- Pearlitic rails are the most widely used and widely used products in the railway sector.
- the existing carbon steel rails and microalloyed rails with over-eutectoid carbon content have a maximum strength of only 1300-1400 MPa even after heat treatment.
- the rail head part is easy to form too fast wear, nuclear injury, peeling off the block and other damage, the service life of the rail is greatly reduced and the driving safety is endangered. Therefore, in the case of irreversible transportation conditions, it is very important to improve the toughness of the rail and thus extend the service life of the rail. For heavy-duty railway small radius curve sections, wear has gradually become the primary factor affecting life.
- the most effective way to improve wear performance is to increase the hardness of the rail.
- the most effective and cheapest way to increase the hardness is to increase the carbon content in the steel.
- an increase in carbon content will result in a decrease in the toughness and plasticity index of the rail, and the existing ductile plasticity is close to the lower limit of the safe service of the rail. If this index is further reduced, the risk of brittle fracture of the rail under the same service conditions will increase.
- the use of heat treatment technology relying on the strong fine grain strengthening effect, can improve the toughness and plasticity of the rail while improving the hardness of the rail. It has been proved that the heat-treated rail usually has higher toughness and comprehensive performance than the hot-rolled rail of the same composition.
- the object of the present invention is to overcome the problem of poor toughness and comprehensive performance of the hypereutectoid steel rail in the prior art, and to provide a hypereutectoid steel rail and a preparation method of the hypereutectoid steel rail.
- the inventors of the present invention found in the course of research that for high carbon content rails, refining the austenite grains and finally refining the pearlite layer spacing not only contributes to the strength, but also has a significant benefit to the improvement of the ductile plasticity index; The final effect of refining austenite grains on toughness and plasticity is far less than that of fine grain strengthening. However, for hypereutectoid steels with higher carbon content, if the ductile plasticity has reached the limit, it can be further refined. Austenitic grains are important for maintaining high strength of the rail while achieving higher toughness and plasticity.
- CN102803536A High-carbon steel rail with excellent ductility and manufacturing method thereof
- 1 low-temperature reheating after rail rolling but there is a problem that coarse carbides remain in the austenite grain inside, On the contrary, the toughness and plasticity of the pearlite structure after the accelerated cooling is lowered.
- reheating also has economic problems such as high manufacturing cost and low production efficiency; 2 the precipitates pin the austenite grain boundaries and refine the austenite grains, thereby improving the toughness of the final rail;
- the effect of the austenitic state on the properties of the final product is limited. However, when the carbon content exceeds 0.85%, the influence of the austenite state on the properties of the product cannot be ignored.
- the inventors of the present invention also found in the research process that if it is desired to refine the austenite grains and finally obtain a rail product with excellent performance, it is necessary to uniformly control the rolling temperature and the finishing temperature to be finally prepared. Rails with excellent toughness and comprehensive performance under eutectoid conditions, if combined with the control of the chemical composition and cooling process of the billet, will produce better performance rails.
- the present invention provides a method of preparing a hypereutectoid steel rail, wherein the method comprises rolling a steel slab containing V and Ti, wherein the steel slab contains 0.85-0.94 by weight based on the total weight of the steel slab % carbon, and start rolling temperature T start and a final finish rolling temperature T and the relationship between the content of vanadium [V] and a titanium content [Ti] satisfy the following formula:
- T final 750 + b ([V] + 5 [Ti]),
- [V] is 0.03-0.08 wt%
- [Ti] is 0.011-0.02 wt%
- [V]+5 [Ti] is 0.12-0.14 wt% based on the total weight of the billet.
- the invention also provides a hypereutectoid steel rail prepared by the above method.
- the hypereutectoid steel rail prepared by the method of the invention has excellent toughness comprehensive properties (such as toughness and contact fatigue resistance), in particular, the microstructure can be obtained as pearlite + trace secondary cementite. Eutectoid rails.
- FIG. 1 is a view showing the microstructure of a hypereutectoid steel rail obtained in Example 1 of the present invention.
- the present invention provides a method of preparing a hypereutectoid steel rail, wherein the method comprises rolling a steel slab containing V and Ti, wherein the steel slab contains 0.85-0.94% by weight based on the total weight of the steel slab carbon, and start rolling temperature T start and a final finish rolling temperature T and the relationship between the content of vanadium [V] and a titanium content [Ti] satisfy the following formula:
- T final 750 + b ([V] + 5 [Ti]),
- [V] is 0.03-0.08 wt%
- [Ti] is 0.011-0.02 wt%
- [V]+5 [Ti] is 0.12-0.14 wt% based on the total weight of the billet.
- C is the most important and cheapest element for improving the hardness and pearlite transformation of pearlite rail.
- the C content is less than 0.85%, even if the accelerated cooling after rolling is used, the high strength and corresponding force required for heavy-duty railway cannot be obtained. Wear resistance; when the C content is more than 0.94%, secondary cementite distributed along the grain boundary will still be precipitated at the prior austenite grain boundary, which deteriorates the impact toughness of the rail, and the contact fatigue resistance of the rail is greatly reduced. Therefore, the C content is limited to 0.85% to 0.94%.
- V When V is at room temperature, the solubility in steel is very low, and in the hot rolling process, such as in the austenite grain boundary or other areas, it is precipitated in the form of fine grained vanadium carbonitride, or in steel. Ti composite precipitation, inhibiting the growth of austenite grains, thereby achieving the purpose of refining the grain to improve performance; when [V] is less than 0.03 wt%, the precipitation of V-containing carbonitride is limited, and it is difficult to exert a strengthening effect; When V] is more than 0.08% by weight, coarse carbonitrides are easily formed, and the ductility of the rail is deteriorated. Therefore, [V] is 0.03-0.08% by weight.
- the main role of Ti in steel is to refine austenite grains during heating, rolling and cooling, and ultimately increase the elongation and stiffness of the rail, which is one of the important additive elements of the present invention.
- [Ti] is less than 0.011% by weight, the amount of carbides formed in the rail is extremely limited; when [Ti] is more than 0.02% by weight, on the one hand, since Ti is a strong carbonitride forming element, the excessive TiC generated will cause The hardness of the rail is too high.
- the TiC is more concentrated and enriched to form coarse carbides, which not only reduces the ductile plasticity, but also makes the contact surface of the rail easy to crack and cause fracture under the impact load. Therefore, [Ti] is from 0.011 to 0.02% by weight.
- V, Ti in steel and C, N and other affinity and the formation of carbides in the number and form are significantly different, but formed
- the role of carbonitrides in refining austenite grains is similar.
- V in a steel with a lower N content, the V content of the solid solution in the ferrite matrix exceeds 50%, and in the steel with a higher N content, the V dissolved in the steel is more than 20%, and the remaining 70 % is precipitated as vanadium carbonitride.
- the improvement of performance by adding V or Ti alone is not significant, such as adding 0.09% of V while the strength of the rail without adding Ti can still reach 1350 MPa, but the elongation is generally less than 10%, and Ti is added separately. Microalloying, the strength of the rail cannot meet the requirement of 1350 MPa, and therefore, the slab of the present invention contains both V and Ti, and [V] + 5 [Ti] is 0.12 - 0.14 wt%.
- [V] is from 0.045 to 0.055% by weight
- [Ti] is from 0.014 to 0.02% by weight
- [V] + 5 [Ti] is from 0.12 to 0.13% by weight.
- the steel slab of the above composition can be obtained by a conventional method in the art, for example, smelting molten steel containing the above components by a converter or an electric furnace, and being subjected to aluminum-free deoxidation, refining outside the furnace, vacuum degassing treatment, and continuous casting to 250 mm ⁇ 250 mm -
- the 450mm ⁇ 450mm section billet is cooled and heated into the heating furnace.
- the billet heating temperature is greater than 1200°C, and the steel billet is heated to no more than 3h to ensure that the billet cross-section billet temperature is evenly discharged, and the scale is removed to obtain the billet of the present invention.
- the specific process I will not repeat them here.
- the size, distribution and morphology of the precipitated phase are significantly different depending on the difference between the rolling temperature and the finishing temperature, and the different [V] and [Ti].
- the rail performance obtained varied significantly, the inventors of the present invention found that, when the start rolling temperature T and the open end and the finishing temperature T [V] +5 [Ti] satisfy the following expression, the steel can be ensured
- the fine and dispersed vanadium carbonitride and titanium carbonitride are fully dissolved and precipitated, so that the prepared hypereutectoid steel rail has excellent toughness and plasticity and contact fatigue resistance.
- 780 ⁇ a ⁇ 800, 470 ⁇ b ⁇ 500 is preferable.
- the steel slab may further contain Si: 0.4 to 0.9% by weight, Mn: 0.7 to 1.3% by weight, Cr: 0.2 to 0.6% by weight, P ⁇ 0.02% by weight, S ⁇ based on the total weight of the slab. 0.00% by weight, N: 0.06-0.09 by weight.
- Si is present as a solid solution strengthening element in steel in the ferrite and austenite to increase the strength of the structure.
- the invention preferably controls the content of Si within the above range, can enhance the solid solution effect, enhance the ductility of the rail, optimize the lateral performance of the rail, and is beneficial to improving the safety of use of the rail.
- Mn can form a solid solution with Fe in the steel slab, and the strength of ferrite and austenite can be improved.
- Mn is a carbide forming element. After entering the cementite, it can partially replace the Fe atom, increase the hardness of the carbide, and finally increase the hardness of the steel.
- it is preferable to control the content of Mn within the above range, and it is possible to prevent the toughness and plasticity from being affected by the excessive hardness of the carbide in the steel while ensuring a high strengthening effect.
- Cr and Fe in the slab can form a continuous solid solution and form a plurality of carbides with C, which is one of the main strengthening elements in the steel.
- Cr can uniform the distribution of carbides in the steel and improve the wear properties of the steel.
- the present invention preferably controls the content of Cr to the above range, which is advantageous for improving the ductility of the rail.
- the N content it is preferred to control the N content to the above range, which is advantageous for improving the toughness and comprehensive properties of the rail under room temperature conditions.
- the slab contains Si: 0.55-0.65 wt%, Mn: 1.25-1.3 wt%, Cr: 0.4-0.55 wt%, P ⁇ 0.014 wt%, S ⁇ based on the total weight of the slab. 0.005 wt%, N: 0.06-0.07 wt.
- the method may further comprise: after the rolling, when the surface layer of the rail head surface temperature T decreases below the final finish rolling temperature T is lower than 20-50 deg.] C, rapid cooling of the rail head When the rapid cooling process causes the rail surface temperature T surface layer to be 450-550 ° C, the rapid cooling is stopped and air cooling is continued to room temperature.
- the cooling rate of the rapid cooling is not particularly limited and may be a conventional choice in the art.
- the cooling rate of the rapid cooling is preferably 2 to 5 ° C / s, preferably 4.5 to 4.9 ° C / s.
- the embodiment of the rapid cooling is not particularly limited and may be a conventional choice in the art.
- the rapid cooling embodiment may be to apply a cooling medium to the top surface and both sides of the rail head of the rail. .
- the selection of the cooling medium is not particularly limited and may be a conventional choice in the art as long as the cooling purpose of the present invention can be attained.
- the cooling medium is a compressed air and/or water mist mixture.
- the present invention also provides a hypereutectoid steel rail prepared by the above method. It should be understood that the hypereutectoid steel rail provided by the present invention has the same composition as the steel slab described above.
- the hypereutectoid steel rail of the invention has excellent toughness and plasticity and contact fatigue resistance.
- room temperature means “25 ° C”.
- the slabs used in the following examples and comparative examples contained chemical compositions as shown in Table 1, in which, with the exception of the elements in Table 1, the balance was Fe and unavoidable impurities:
- the 1# to 6# billets in Table 1 were rolled into 60 kg/m rails according to the rolling and rapid cooling processes shown in the corresponding numbers in Table 2, and rapidly cooled by compressed air, and then the above-mentioned finished rails were air-cooled to At room temperature, hypereutectoid rails A1 to A6 were obtained.
- the 1# to 6# billets in Table 1 were rolled into 60 kg/m steel rails according to the rolling and rapid cooling processes shown in the corresponding numbers in Table 3, and rapidly cooled by compressed air, and then the above-mentioned finished rails were air-cooled to At room temperature, hypereutectoid rails D1 to D6 were obtained.
- microstructure Inspection Method the microstructure of the hypereutectoid rail was measured by MeF3 optical microscope. The microstructure was measured as shown in Table 4. The microstructure of A1 is shown in Figure 1. Show.
- P+Fe 3 C II (micro) refers to pearlite + trace secondary cementite
- P+Fe 3 C II (less) refers to pearlite + small amount of secondary cementite
- trace and “small amount” “It is a relative relationship, and the "trace” indicates less amount relative to "small amount”, mainly to show that the secondary cementite in the microstructure of the hypereutectoid rail in the embodiment is less than that in the comparative example.
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Abstract
Description
Claims (10)
- 一种制备过共析钢轨的方法,其特征在于,该方法包括将含有V和Ti的钢坯进行轧制,其中,以钢坯的总重量为基准,所述钢坯含有0.85-0.94重量%的碳,开轧温度T开和终轧温度T终与钒含量[V]和钛含量[Ti]的关系满足以下公式:T开=1100+a([V]+5[Ti]),T终=750+b([V]+5[Ti]),其中,500≤a≤800,300≤b≤500;以钢坯的总重量为基准,[V]为0.03-0.08重量%,[Ti]为0.011-0.02重量%,且[V]+5[Ti]为0.12-0.14重量%。
- 根据权利要求1所述的方法,其中,[V]为0.045-0.055重量%,[Ti]为0.014-0.02重量%,且[V]+5[Ti]为0.12-0.13重量%。
- 根据权利要求1或2所述的方法,其中,以钢坯的总重量为基准,所述钢坯还含有Si:0.4-0.9重量%,Mn:0.7-1.3重量%,Cr:0.2-0.6重量%,P≤0.02重量%,S≤0.008重量%,N:0.06-0.09重量‰。
- 根据权利要求3所述的方法,其中,以钢坯的总重量为基准,所述钢坯含有Si:0.55-0.65重量%,Mn:1.25-1.3重量%,Cr:0.4-0.55重量%,P≤0.014重量%,S≤0.005重量%,N:0.06-0.07重量‰。
- 根据权利要求1或2所述的方法,其中,所述方法还包括:在轧制之后,当轨头表层温度T表层降低至比终轧温度T终低20-50℃时,对轨头进行快速冷却;当所述快速冷却的过程使得轨头表层温度T表层为450-550℃时,停止快速冷却并继续空冷至室温。
- 根据权利要求5所述的方法,其中,所述快速冷却的冷却速度为2-5℃/s。
- 根据权利要求6所述的方法,其中,所述快速冷却的冷却速度为4.5-4.9℃/s。
- 根据权利要求5所述的方法,其中,所述快速冷却的实施方式是在所述钢轨的轨头顶面和两个侧面施加冷却介质。
- 根据权利要求8所述的方法,其中,所述冷却介质为压缩空气和/或水 雾混合液。
- 由权利要求1-9中任意一项所述的方法制备得到的过共析钢轨。
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BR112019000331-2A BR112019000331A2 (pt) | 2016-07-14 | 2017-05-24 | trilho hipereutectoide e método de produção do mesmo |
AU2017295527A AU2017295527B2 (en) | 2016-07-14 | 2017-05-24 | A hypereutectoid rail and manufacturing method thereof |
US16/317,416 US20190226040A1 (en) | 2016-07-14 | 2017-05-24 | Hypereutectoid rail and manufacturing method thereof |
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CN201610552631.3A CN106086663B (zh) | 2016-07-14 | 2016-07-14 | 一种过共析钢轨及其制备方法 |
CN201610552631.3 | 2016-07-14 |
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CN106086663B (zh) * | 2016-07-14 | 2018-03-06 | 攀钢集团攀枝花钢铁研究院有限公司 | 一种过共析钢轨及其制备方法 |
CN107675084B (zh) * | 2017-10-10 | 2019-05-10 | 攀钢集团研究院有限公司 | 高碳高强韧性珠光体钢轨及其制造方法 |
CN107739806B (zh) * | 2017-10-10 | 2019-10-11 | 攀钢集团研究院有限公司 | 高韧塑性过共析钢轨及其制造方法 |
CN107739983A (zh) * | 2017-10-30 | 2018-02-27 | 攀钢集团攀枝花钢铁研究院有限公司 | 一种过共析钢轨及其生产方法 |
CN107747040A (zh) * | 2017-10-31 | 2018-03-02 | 攀钢集团攀枝花钢铁研究院有限公司 | 耐腐蚀高速铁路钢轨制备方法 |
CN107779768A (zh) * | 2017-10-31 | 2018-03-09 | 攀钢集团攀枝花钢铁研究院有限公司 | 用于生产耐腐蚀高速铁路用钢轨的方法 |
CN112718855A (zh) * | 2020-11-30 | 2021-04-30 | 攀钢集团攀枝花钢铁研究院有限公司 | 一种过共析钢轨及其制备方法 |
CN115094338B (zh) * | 2022-07-27 | 2023-09-22 | 内蒙古科技大学 | 一种过共析钢轨用钢及其制备方法 |
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BR112019000331A2 (pt) | 2019-04-16 |
US20190226040A1 (en) | 2019-07-25 |
CN106086663B (zh) | 2018-03-06 |
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