CN116043114B - High-toughness alloy forged steel for high-speed rail brake disc with speed of 400 km per hour, heat treatment method and production method thereof - Google Patents

High-toughness alloy forged steel for high-speed rail brake disc with speed of 400 km per hour, heat treatment method and production method thereof Download PDF

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CN116043114B
CN116043114B CN202310045633.3A CN202310045633A CN116043114B CN 116043114 B CN116043114 B CN 116043114B CN 202310045633 A CN202310045633 A CN 202310045633A CN 116043114 B CN116043114 B CN 116043114B
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brake disc
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steel
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陈世杰
汪开忠
胡芳忠
杨志强
杨少朋
陈恩鑫
庄振
金国忠
景宏亮
王自敏
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Maanshan Iron and Steel Co Ltd
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Abstract

The invention discloses a high-toughness alloy forged steel for a high-speed high-iron brake disc with a speed of 400 km per hour, and a heat treatment method and a production method thereof, wherein the high-toughness alloy forged steel for the high-speed high-iron brake disc with the speed of 400 km per hour comprises the following components: C. si, mn, cr, mo, ni, cu, nb, W, ti, V, al the mechanical properties at normal temperature are that the tensile strength is more than or equal to 1200MPa, the yield strength is more than or equal to 1100MPa, A is more than or equal to 17%, Z is more than or equal to 65%, and KV at 20 ℃ is obtained by controlling the relational values among the contents of all chemical components and part of chemical components 2 The high-toughness alloy forged steel for the high-iron brake disc with the speed per hour of 400 km and excellent cold and hot fatigue performance has the tensile strength of more than or equal to 150J and more than or equal to 600MPa at 700 ℃, and no crack is generated after the high-toughness alloy forged steel is subjected to cold and hot circulation for 1000 times at 800-20 ℃.

Description

High-toughness alloy forged steel for high-speed rail brake disc with speed of 400 km per hour, heat treatment method and production method thereof
Technical Field
The invention belongs to the field of alloy forged steel for brake discs, and particularly relates to high-toughness alloy forged steel for high-speed rail brake discs with a speed of 400 km/h, and a heat treatment method and a production method thereof.
Background
In recent years, the world rapid transit railway is rapidly developed, and the degree of high speed is higher and higher. With the increase of train speed, higher demands are being placed on the braking devices and the braking materials. For high speed trains, the large energy generated by braking is dissipated by the foundation braking element in a short period of time, which is a significant and critical issue. The brake disc is a core component in a basic brake device, plays an important role, and huge heat load, thermal shock and thermal cycle generated in the braking process can lead to the phenomena of reduced disc body manufacturing efficiency, high-temperature abrasion, thermal fatigue failure and the like, so that the steel for the brake disc is required to have excellent normal temperature performance, good high temperature performance, heat conduction performance and cold-hot fatigue performance.
The high-speed railway brake disc is used as an important part for ensuring the safe operation of the high-speed railway, and currently common materials of the high-speed railway brake disc in the world comprise AISI 4330, 28CrMoV5-08, 15CDV6 and the like, and the materials can meet the requirements of trains with the speed of 350 km per hour and below and cannot be applied to trains with higher speed per hour. With the rapid development of rail transportation industry, the rapid construction of coastal high-speed rails causes higher requirements on steel for brake discs of high-speed trains, and development of brake disc materials with excellent normal temperature, high temperature performance and thermal fatigue performance is urgently needed.
At present, most high-speed trains use cast steel or forged steel brake discs, but composite brake discs are still in a research and development stage and cannot be widely popularized and applied. And the cast steel brake disc has higher cost due to more alloy elements. The related patents disclosed in China mainly relate to the normal-temperature mechanical properties of the brake disc material of the high-speed train, and the fresh patents relate to the high-temperature properties and cold-hot fatigue resistance of the brake disc material, and the toughness of the brake disc material is difficult to consider while the high-temperature mechanical properties of the brake disc material are improved. The high-speed train brake disc material with excellent comprehensive mechanical properties and fatigue resistance is developed, and has important significance for improving the service performance and service life of the brake disc, realizing localization of the brake disc of the high-speed train and ensuring the running safety of the train.
Chinese patent CN105779893B discloses an alloy cast steel for a brake disc of a high-speed train and a brake disc of a high-speed train manufactured from the alloy cast steel, which is characterized in that C0.18% -0.26% by weight; si 0.30-0.50%; mn 0.68-1.40%; p is less than or equal to 0.025%; s is less than or equal to 0.013 percent; cr 1.10-1.82%; 0.90 to 1.50 percent of Ni; mo 0.65-1.02%; v is 0.22 to 0.34 percent; the sum of the contents of other components is less than or equal to 0.30 percent, wherein W is less than 0.1 percent; fe is the balance; normalizing at 900-980 deg.c for 3.5-5 hr, water quenching at 900-980 deg.c for 3.5-5 hr, and tempering at 580-650 deg.c for 3.5-5 hr, and the alloy cast steel has the following mechanical performance indexes after heat treatment: tensile strength is equal to or more than 1050MPa; yield strength is more than or equal to 935MPa; the elongation is more than or equal to 14%; the area shrinkage rate is more than or equal to 35 percent. The alloy cast steel has the defect that the crack length of the V-shaped notch is about 0.31mm after 600 times of 600-20 ℃ cold and hot fatigue tests, and the strength, toughness and cold and hot fatigue performance cannot meet the requirements of a high-speed iron brake disc with 400 km per hour.
Chinese patent CN111360198B discloses a cast steel for high-toughness cold-hot fatigue resistant high-speed train brake disc and preparation method,the composite material is characterized by comprising the following chemical components in percentage by weight: 0.20 to 0.40 percent, si:0.30 to 0.70 percent, mn:0.50 to 2.00 percent, P is less than or equal to 0.015 percent, S is less than or equal to 0.010 percent, cr:0.50 to 2.00 percent of Ni:0.50 to 2.00 percent of Mo: 0.40-1.80%, nb:0.010 to 0.030 percent, V:0.01 to 0.30 percent, N is less than or equal to 0.015 percent, O is less than or equal to 0.010 percent, and the balance is Fe and residual trace impurities; the total content of Mn+Cr+Ni is 2.00-6.00%, and the total content of Mo+V is 0.71-1.35%. The cast steel material has room temperature mechanical properties: the yield strength is more than or equal to 1000MPa, the tensile strength is more than or equal to 1100MPa, the elongation after breaking is more than or equal to 12.0%, and the room temperature impact absorption power (KV) 2 ) More than or equal to 50J;600 ℃ high temperature mechanical properties: the yield strength is more than or equal to 500MPa, and the tensile strength is more than or equal to 550MPa. The defect is that the normal temperature mechanical property and the high temperature property of the steel are not enough to meet the requirement of a high-speed rail brake disc with the speed of 400 km per hour.
Chinese patent CN107760992a discloses a steel for brake disc of tungsten-containing high-speed train, which is characterized in that the percentage of chemical components is C:0.20 to 0.30 percent, si:0.20 to 0.40 percent, mn:0.20 to 0.40 percent, P is less than or equal to 0.010 percent, S is less than or equal to 0.005 percent, cr:0.90 to 1.50 percent, ni is less than or equal to 0.20 percent, mo:0.40 to 0.90 percent, al is less than or equal to 0.025 percent, V: 0.70-1.00%, W: 0.70-1.20%, cu less than or equal to 0.20%, N less than or equal to 0.0050, and the balance Fe and residual trace impurities, the material has excellent high-temperature performance, the tensile strength at 500 ℃ is more than or equal to 1000MPa, the tensile strength at 600 ℃ is more than or equal to 900MPa, the toughness and the high-temperature performance above 600 ℃ of the material are not characterized, the whole heat treatment temperature is higher, the quenching and tempering temperature interval is narrower, and the industrial mass production is not facilitated.
At present, although the research of the steel for the high-speed railway brake disc in China has a certain accumulation, the steel can only meet the requirement of a train with the speed of 350 km per hour and below, and the research on the brake disc of the high-speed train with the speed of 400 km per hour and above is almost blank. With the speed of Gao Tiedi, development of steel for high-speed railway brake disks having high strength and toughness, good high-temperature performance and excellent thermal fatigue performance is urgently required.
Disclosure of Invention
The invention aims to provide high-toughness alloy forged steel for a high-speed rail brake disc with a speed of 400 km/h, a heat treatment method and a production method thereof, and a steel plate for a high-speed rail brake disc with a speed of 400 km/hThe relative formula values among the contents of all chemical components and part of the chemical components are controlled to obtain the product with the mechanical properties of tensile strength of more than or equal to 1200MPa, yield strength of more than or equal to 1100MPa, A of more than or equal to 17%, Z of more than or equal to 65% and KV at 20 DEG C 2 The high-toughness alloy forged steel for the high-iron brake disc with the speed per hour of 400 km and excellent cold and hot fatigue performance has the tensile strength of more than or equal to 150J and more than or equal to 600MPa at 700 ℃, and no crack is generated after the high-toughness alloy forged steel is subjected to cold and hot circulation for 1000 times at 800-20 ℃.
In order to achieve the above purpose, the technical scheme adopted by the invention is as follows:
a high-toughness alloy forged steel for a high-speed iron brake disc with a speed of 400 km/h comprises the following components in percentage by weight: 0.18 to 0.25 percent of C, 0.15 to 0.40 percent of Si, 0.40 to 0.80 percent of Mn, 0.90 to 1.30 percent of Cr, 0.90 to 1.20 percent of Mo, 0.50 to 0.70 percent of Ni, 0.20 to 0.50 percent of Cu, 0.010 to 0.040 percent of Nb, and W:0.30 to 0.60 percent of Ti: 0.040-0.080 percent, 0.25-0.35 percent of V, 0.015-0.040 percent of Al, less than or equal to 0.015 percent of P, less than or equal to 0.010 percent of S, less than or equal to 0.0070 percent of N, less than or equal to 0.0015 percent of T.O, and the balance of Fe and other unavoidable impurities;
wherein,
36.5≤λ 700℃ ＝32.65+0.25W-2.2V+0.64Mo+0.35Cr+17Cu-1.08Ni-1.66Mn-3.67Si+4.52C≤38.5；
14≤X＝6％C+4％Cr+3.6％Mo+2.8％Ni+3.2％W+24％Nb+28％Ti+3.5％V≤18。
the metallographic structure of the high-toughness alloy forged steel for the high-speed iron brake disc with the speed per hour of 400 km is tempered sorbite.
The high-toughness alloy forged steel for the high-speed iron brake disc with the speed per hour of 400 km has the tensile strength of more than or equal to 1200MPa, the yield strength of more than or equal to 1100MPa, A of more than or equal to 17%, Z of more than or equal to 65% and KV of 20 DEG C 2 More than or equal to 150J, and the tensile strength at 700 ℃ is more than or equal to 600MPa; after 1000 times of cold and hot circulation at 800-20 ℃, no crack is generated.
The heat treatment method of the high-toughness alloy forged steel for the high-speed rail brake disc with the speed per hour of 400 km comprises the following steps:
(1) Normalizing: heating the brake disc to 910-1000 ℃, preserving heat, and then air-cooling; through the normalizing treatment, the alloy elements in the steel for the brake disc are fully and uniformly dissolved, so that preparation is made for subsequent quenching and tempering;
(2) Quenching: heating the brake disc to 870-950 ℃, preserving heat, and then water-cooling to ensure that the austenite grain size in the steel is moderate;
(3) Tempering: heating the brake disc to 580-660 ℃, preserving heat, then air-cooling, eliminating internal structural stress through tempering, fully precipitating carbide in the steel, ensuring moderate carbide size, ensuring that the steel for the brake disc has excellent toughness matching, improving the structural stability of the steel in the quenching and rapid heating process, and improving the high-temperature performance of the steel.
In the normalizing process, the heating speed is 100-160 ℃/h, the heat preservation time t is determined by the thickness delta of a brake disc, t=1.5-2.5 delta, the unit of t is min, and the unit of delta is mm.
In the quenching process, the heating speed is 100-160 ℃/h, the heat preservation time t is determined by the thickness delta of a brake disc, t=1.0-1.2 delta, the unit of t is min, and the unit of delta is mm.
In the tempering process, the heating speed is 50-110 ℃/h, the heat preservation time t is determined by the thickness delta of the brake disc, t=2.0-4.0 delta, the unit of t is min, and the unit of delta is mm.
The production method of the high-toughness alloy forged steel for the high-speed iron brake disc with the speed per hour of 400 km comprises the following steps: smelting in an arc furnace or a converter, refining in an LF furnace, vacuum degassing in RH or VD, continuous casting, heating in a casting blank heating furnace, rolling round steel for a brake disc, forging a brake disc blank, heat treatment, machining, flaw detection, packaging and warehousing, wherein the heat treatment process is carried out by adopting the heat treatment method.
The high-toughness alloy forged steel for the high-speed rail brake disc with the speed of 400 km/h comprises the following components:
c: c is the least expensive strengthening element in the steel, and each 0.1% of solid solution C can improve the strength by about 450MPa, and the C and the alloy element in the steel form a precipitated phase to play a role in precipitation strengthening. C can obviously improve the hardenability, but as the content of C increases, the plasticity and toughness decrease, so the content of C is controlled to be 0.18-0.25%.
Si: si is an effective solid solution strengthening element in steel, improves the strength and the hardness of the steel, can play a deoxidizing role in steelmaking, and is a common deoxidizer. However, si tends to be biased at austenite grain boundaries, which reduces the grain boundary binding force and causes brittleness. In addition, si tends to cause element segregation in steel. Therefore, the Si content is controlled to be 0.15% to 0.40%.
Mn: mn can play a solid solution strengthening role, the solid solution strengthening capability is weaker than that of Si, mn is an austenite stabilizing element, the hardenability of steel can be obviously improved, decarburization of steel can be reduced, and the combination of Mn and S can prevent hot shortness caused by S. However, excessive Mn can reduce the plasticity of the steel, and simultaneously can easily cause austenite-martensite transformation in the repeated heating and cooling process, so that the thermal expansion coefficient and the heat conduction coefficient are shock-changed, and the cold-hot fatigue performance of the brake disc is reduced. Therefore, the Mn content is controlled to be 0.40-0.80%.
Cr: cr is a carbide forming element, can improve the hardenability, strength and wear resistance of steel, can improve the high-temperature performance and fatigue resistance of steel, is an important alloy element of heat-resistant steel, but is easy to cause tempering brittleness, and can increase reheat crack sensitivity when the Cr content is too high. The Cr content should be controlled to be 0.90% -1.30%.
Mo: mo mainly improves the hardenability and the heat strength of steel, maintains enough strength and creep resistance at high temperature, ensures that the structure of the steel can maintain higher stability in the tempering process, and can effectively reduce the segregation of impurity elements such As P, S, as and the like at grain boundaries, thereby improving the toughness of the steel and reducing the tempering brittleness. Mo can improve the strength of steel by the combined action of solid solution strengthening and precipitation strengthening, and can also change the toughness of steel by changing the precipitation of carbide. Mo is controlled to be 0.90-1.20%.
Ni: ni can form infinite mutual-soluble solid solution with Fe, is an austenite stabilizing element, has the effect of expanding a phase area, increases the stability of supercooled austenite, makes a C curve move right, and improves the hardenability of steel. Ni can refine the width of the martensite lath and improve the strength. Ni is used for obviously reducing the ductile-brittle transition temperature of steel and improving the low-temperature toughness. With the increase of the nickel content, the normal temperature strength and the high temperature strength of the steel are increased, but the influence on the plasticity and the toughness is not great, but the Ni element is a noble metal element, and excessive addition causes excessive cost. The Ni content is controlled to be 0.50-0.70%.
Nb: nb is a strong C, N compound forming element, nb (C, N) is finely dispersed and maintains a coherent relation with the matrix, so that the matrix can play a role in strengthening and refining tissues, and the strengthening of the matrix can increase the fatigue crack initiation and propagation resistance, thereby improving the fatigue strength. The Nb content is controlled to be 0.010-0.040 percent.
Ti: ti is a strong carbide forming element, and the addition of a proper amount of titanium into steel can obviously refine structural grains, improve strength and toughness, and particularly has obvious contribution to improving impact toughness. The Ti content is controlled to be 0.040-0.080 percent.
V: v is a widely used microalloying element that has the effect of preventing austenite grain growth when heated. The addition of vanadium prevents the growth of austenite grains by the precipitation of V (C, N) and the grain boundary pinning of undissolved V (C, N) particles, thereby improving the toughness of the steel, but at the same time, reducing the hardenability of the steel. The research results show that the V content is about 0.30 percent, and the effect of improving the high-temperature strength is most obvious, so that the V content is controlled to be 0.25 to 0.35 percent.
Nb, ti, V are the most commonly used microalloying elements, which in turn decrease the pinning effect on grain boundaries. The addition of Nb, ti, V and other alloys can form carbonitride, and the steel is strengthened through dissolution-precipitation behavior in the heating and cooling processes of the steel, and in addition, microalloy elements exist in the steel in the form of substitutional solute atoms, are easy to be aggregated on dislocation lines, generate strong dragging action on the dislocation, and finally play a strong role in preventing recrystallization.
Cu: cu has a solid solution strengthening effect, and the solid solution strengthening degree is similar to Mn. However, cu produces high crack sensitivity in the steel, which reduces the cold and hot fatigue performance of the brake disc. The Cu content is controlled to be 0.20-0.50%.
W: w is a strong carbide forming element, so that the high-temperature strength and heat resistance of the steel are improved, and the content of W is controlled to be 0.30-0.60%.
Al: al is a stronger deoxidizing element and forms an AlN precipitated phase with N element in steel to have the effect of inhibiting grain growth, but the high-temperature performance is reduced due to the ultra-fine grains, and the content of Al is controlled to be 0.015% -0.040%.
P and S: sulfur easily forms MnS inclusions with manganese in the steel, so that the steel is thermally brittle; p is an element with strong segregation tendency, increases the cold brittleness of steel, reduces plasticity, and is harmful to uniformity of product structure and performance. Controlling P to be less than or equal to 0.015 percent and S to be less than or equal to 0.010 percent.
T.o and N: T.O forms oxide inclusion in steel, and T.O is controlled to be less than or equal to 0.0015%; the excessive N content in the V, al steel promotes the precipitation of carbon VN and AlN in austenite, refines austenite grains and reduces tempering resistance of the steel, and simultaneously N also reduces cold working performance of the steel, and N is controlled to be less than or equal to 0.0070 percent.
The heat conductivity of pure iron gradually decreases along with the rise of temperature, and the influence of different alloy elements in steel on the heat conductivity is different, so that the steel still has good heat conductivity under the high temperature condition, the problem that the heat generated by braking in the high-speed emergency braking process cannot be quickly conducted to cause local overheating and fatigue failure is avoided, the proportion of C, si, mn, cr, ni, mo, V, W, cu is limited, and the steel still has higher heat conductivity at high temperature is ensured. The impurity elements such as P, S have great influence on the heat conductivity coefficient of the steel, but the P, S content is extremely low in the invention, so the influence is negligible. The addition of the C atoms distributes more strong carbide forming elements and weak carbide forming elements such as Mn from the matrix of the steel into the carbide, so that the influence of the elements on the heat conductivity is weakened, and the influence coefficient of the C content on the heat conductivity is higher and is 4.52. The significant difference in the electronic structure of the outer layers of the semiconductor element Si and the base Fe results in a significant reduction in the thermal conductivity of the steel, so the Si coefficient is-3.67. The influence of carbide forming elements on the heat conductivity is weaker than that of non-carbide forming elements, and the carbide forming elements have different contribution coefficients according to different contribution degrees of different alloy elements on the heat conductivity, so that the calculation formula of the heat conductivity of the steel at the high temperature of 700 ℃ is as follows:
λ 700℃ ＝32.65+0.25W-2.2V+0.64Mo+0.35Cr+17Cu-1.08Ni-1.66Mn-3.67Si+4.52C。
in order to ensure that the steel still has good heat conduction performance under the high temperature (700 ℃), the heat conduction coefficient should accord with the lambda of 36.5 or less 700℃ ≤38.5。
Wherein, the numerical value part of the element percentage is directly adopted in calculation.
In order to ensure that the steel has better high-temperature strength, the addition amount of C, cr, mo, ni, W, nb, ti, V alloy meets the requirement of a component range, and according to the contribution degree of each alloy element to the high-temperature strength, the addition amount also accords with the range of being more than or equal to 14 and less than or equal to 18, wherein X=6C+4Cr+3.6Mo+2.8Ni+3.2W+24Nb+28Ti+3.5V.
Compared with the prior art, the high-toughness alloy forged steel for the high-speed iron brake disc with the speed of 400 km per hour has excellent normal temperature performance, high temperature performance and cold and hot fatigue performance, and is suitable for manufacturing high-speed iron brake discs with the speed of 400 km per hour and above
Drawings
Fig. 1 shows a metallographic structure of a high-toughness alloy forged steel for a high-speed railway brake disc at a speed of 400 km/h in example 1.
Detailed Description
The invention provides high-toughness alloy forged steel for a high-speed iron brake disc with a speed of 400 km per hour, which comprises the following components in percentage by weight: 0.18 to 0.25 percent of C, 0.15 to 0.40 percent of Si, 0.40 to 0.80 percent of Mn, 0.90 to 1.30 percent of Cr, 0.90 to 1.20 percent of Mo, 0.50 to 0.70 percent of Ni, 0.20 to 0.50 percent of Cu, 0.010 to 0.040 percent of Nb, and W:0.30 to 0.60 percent of Ti: 0.040-0.080 percent, 0.25-0.35 percent of V, 0.015-0.040 percent of Al, less than or equal to 0.015 percent of P, less than or equal to 0.010 percent of S, less than or equal to 0.0070 percent of N, less than or equal to 0.0015 percent of T.O, and the balance of Fe and other unavoidable impurities;
wherein,
36.5≤λ 700℃ ＝32.65+0.25W-2.2V+0.64Mo+0.35Cr+17Cu-1.08Ni-1.66Mn-3.67Si+4.52C≤38.5；
14≤X＝6％C+4％Cr+3.6％Mo+2.8％Ni+3.2％W+24％Nb+28％Ti+3.5％V≤18。
the heat treatment method of the high-toughness alloy forged steel for the high-speed rail brake disc with the speed per hour of 400 km comprises the following steps:
(1) Normalizing: heating the brake disc to 910-1000 ℃, preserving heat, and then air-cooling; through the normalizing treatment, the alloy elements in the steel for the brake disc are fully and uniformly dissolved, so that preparation is made for subsequent quenching and tempering;
(2) Quenching: heating the brake disc to 870-950 ℃, preserving heat, and then water-cooling to ensure that the austenite grain size in the steel is moderate;
(3) Tempering: heating the brake disc to 580-660 ℃, preserving heat, then air-cooling, eliminating internal structural stress through tempering, fully precipitating carbide in the steel, ensuring moderate carbide size, ensuring that the steel for the brake disc has excellent toughness matching, improving the structural stability of the steel in the quenching and rapid heating process, and improving the high-temperature performance of the steel.
In the normalizing process, the heating speed is 100-160 ℃/h, the heat preservation time t is determined by the thickness delta of a brake disc, t=1.5-2.5 delta, the unit of t is min, and the unit of delta is mm.
In the quenching process, the heating speed is 100-160 ℃/h, the heat preservation time t is determined by the thickness delta of a brake disc, t=1.0-1.2 delta, the unit of t is min, and the unit of delta is mm.
In the tempering process, the heating speed is 50-110 ℃/h, the heat preservation time t is determined by the thickness delta of the brake disc, t=2.0-4.0 delta, the unit of t is min, and the unit of delta is mm.
The production method of the high-toughness alloy forged steel for the high-speed rail brake disc with the speed per hour of 400 km comprises the following steps: smelting in an arc furnace or a converter, refining in an LF furnace, vacuum degassing in RH or VD, continuous casting, heating in a casting blank heating furnace, rolling round steel for a brake disc, forging a brake disc blank, heat treatment, machining, flaw detection, packaging and warehousing, wherein the heat treatment process is carried out by adopting the heat treatment method.
The present invention will be described in detail with reference to examples.
The chemical compositions and weight percentages of the alloy forged steels for high-speed railway brake disks in the examples and comparative examples are shown in table 1.
Table 1 chemical composition (wt%) of examples and comparative examples
The production process of the alloy wrought steel for the high-speed railway brake disc in each example and comparative example is as follows:
smelting in an electric furnace: oxygen is fixed before tapping, and steel retaining operation is adopted in the tapping process, so that slag discharging is avoided;
LF furnace: C. si, mn, cr, ni, mo, cu, nb, V, W, ti and other elements to target values;
vacuum degassing: the pure degassing time is more than or equal to 15 minutes, the H content after vacuum treatment is less than or equal to 1.5ppm, and the phenomenon of hydrogen embrittlement caused by white spots in steel is avoided;
continuous casting: the target temperature of the ladle molten steel is controlled to be 10-40 ℃ above the liquidus temperature, and round billets with phi 380-700 mm are continuously cast.
Rolling route: round billet heating, high-pressure water descaling, cogging, hot rolling round steel and slow cooling; wherein the rolling ratio during hot rolling is more than or equal to 3:1.
Forging route: round steel heating and brake disc blank forging.
Brake disc processing route: rough machining of a blank, normalizing, quenching and tempering heat treatment, finish machining, grinding, flaw detection, packaging and warehousing.
Wherein the heat treatment process is shown in table 2.
TABLE 2
The mechanical properties of the alloy forged steel for high-speed railway brake disks in each example and comparative example are shown in table 3.
TABLE 3 Table 3
The service condition of the brake disc is simulated, the test sample is heated to 800 ℃, the test sample is quickly placed into water with the temperature of 20 ℃ after being kept warm for a period of time, and after repeated heating and cooling for 1000 times, whether cracks are generated or not is observed under a metallographic microscope. The cracking conditions for the examples and comparative examples are shown in Table 4.
TABLE 4 Cold and hot fatigue performance test cases list for examples and comparative examples of the present invention
Steel grade Test parameters Detection situation
Example 1 800-20 ℃ cold-hot circulation 1000 times No crack
Example 2 800-20 ℃ cold-hot circulation 1000 times No crack
Example 3 800-20 ℃ cold-hot circulation 1000 times No crack
Comparative example 1 800-20 ℃ cold-hot circulation 1000 times 896 cracks occurred
Comparative example 2 800-20 ℃ cold-hot circulation 1000 times 835 times crack
Comparative example 3 800-20 ℃ cold-hot circulation 1000 times 779 times crack
Comparative example 4 800-20 ℃ cold-hot circulation 1000 times 814 cracks appear
Comparative example 5 800-20 ℃ cold-hot circulation 1000 times 793 times crack
The chemical composition and the production method of the alloy forged steel for the high-speed railway brake disc in the examples 1 to 3 are properly controlled, and the chemical composition ensures
36.5≤λ 700℃ ＝32.65+0.25W-2.2V+0.64Mo+0.35Cr+17Cu-1.08Ni-1.66Mn-3.67Si+4.52C≤38.5，
X=6%C+4%Cr+3.6%Mo+2.8%Ni+3.2%W+24%Nb+28%Ti+3.5%V is less than or equal to 18, the normal temperature performance, high temperature performance and cold and hot fatigue performance of the steel are all good, and the use requirement of a high-speed iron brake disc with a speed per hour of 400 km and above can be completely met.
The chemical components in comparative examples 1 to 4 are unsuitable forThe heat treatment process of the ratios 3 and 5 is not suitable. In comparative example 1, although the content of each chemical component was controlled within the range of the present application, due to lambda 700℃ And X are both higher than the range defined by the invention, resulting in a material with lower room temperature strength and lower final high temperature performance. In comparative example 2, although the content of each chemical component was controlled within the range of the present application, due to lambda 700℃ And X is lower than the range defined by the invention, so that the normal temperature strength and the high temperature strength of the material can not meet the requirements. In comparative example 3, although the content of each chemical component was controlled within the range of the present application, due to lambda 700℃ The method is lower than the range defined by the invention, and the heat treatment process is unreasonable, so that the overall performance of the material is not ideal. Comparative example 4 although the coefficient of thermal conductivity lambda 700℃ Higher, but the final material strength cannot meet the requirements due to unreasonable control of the components. Comparative example 5 has a reasonable chemical composition, but the heat treatment process is not reasonable, and the strength and cold and hot fatigue properties are also poor.
The foregoing detailed description of a high toughness alloy wrought steel for high speed 400 km/h brake discs, and a heat treatment method and a production method thereof, with reference to the examples, is illustrative and not limiting, and several examples can be enumerated in accordance with the limited scope, thus variations and modifications, without departing from the general inventive concept, shall fall within the scope of protection of the present invention.

Claims (9)

1. A high-toughness alloy forged steel for a high-speed iron brake disc with a speed of 400 km/h is characterized by comprising the following components in percentage by weight: 0.18 to 0.25 percent of C, 0.15 to 0.40 percent of Si, 0.40 to 0.80 percent of Mn, 0.90 to 1.30 percent of Cr, 0.90 to 1.20 percent of Mo, 0.50 to 0.70 percent of Ni, 0.20 to 0.50 percent of Cu, 0.010 to 0.040 percent of Nb, and W:0.30 to 0.60 percent of Ti: 0.040-0.080 percent, 0.25-0.35 percent of V and Al
0.015-0.040%, P less than or equal to 0.015%, S less than or equal to 0.010%, N less than or equal to 0.0070%, T.O less than or equal to 0.0015%, and the balance of Fe and other unavoidable impurities;
wherein,
36.5≤λ 700℃ ＝32.65+0.25W-2.2V+0.64Mo+0.35Cr+17Cu-1.08Ni-1.66Mn-3.67Si+4.52C≤38.5；
14≤X＝6C+4Cr+3.6Mo+2.8Ni+3.2W+24Nb+28Ti+3.5V≤18；
the high-toughness alloy forged steel for the high-speed iron brake disc with the speed per hour of 400 km has the tensile strength of more than or equal to 1200MPa, the yield strength of more than or equal to 1100MPa and no crack after 1000 times of cold-hot circulation at 800-20 ℃.
2. The high-toughness alloy forged steel for high-speed 400 km/h brake disks according to claim 1, wherein a metallographic structure of the high-toughness alloy forged steel for high-speed 400 km/h brake disks is tempered sorbite.
3. The high-toughness alloy forged steel for high-speed 400 km/h brake disks according to claim 1, wherein A is not less than 17%, Z is not less than 65%,
20℃KV 2 more than or equal to 150J, and the tensile strength at 700 ℃ is more than or equal to 600MPa.
4. A heat treatment method of high toughness alloy forged steel for high speed rail brake disc of 400 km/h according to any one of claims 1 to 3, wherein the heat treatment method comprises the steps of:
(1) Normalizing: heating the brake disc to 910-1000 ℃, preserving heat, and then air-cooling;
(2) Quenching: heating the brake disc to 870-950 ℃, preserving heat, and then water-cooling;
(3) Tempering: heating the brake disc to 580-660 ℃, preserving heat, and then air-cooling.
5. The heat treatment method according to claim 4, wherein in the normalizing process, the heating rate is 100-160 ℃/h, the holding time t is determined by the thickness δ of the brake disc, t=1.5-2.5 δ, t is in min, and δ is in mm.
6. The heat treatment method according to claim 4, wherein in the quenching process, the heating rate is 100-160 ℃/h, the holding time t is determined by the thickness delta of the brake disc, t=1.0-1.2 delta, t is in min, and delta is in mm.
7. The heat treatment method according to claim 4, wherein in the tempering process, the heating rate is 50-110 ℃/h, the holding time t is determined by the thickness δ of the brake disc, t=2.0-4.0 δ, t is in min, and δ is in mm.
8. A method for producing a high-toughness alloy forged steel for high-speed rail brake disks having a speed per hour of 400 km as claimed in any one of claims 1 to 3, comprising the steps of: smelting in an arc furnace or a converter, refining in an LF furnace, vacuum degassing in RH or VD, continuous casting, heating in a casting blank heating furnace, rolling round steel for a brake disc, forging a brake disc blank, heat treatment, machining, flaw detection, packaging and warehousing.
9. The production method according to claim 8, wherein the heat treatment process is performed by the heat treatment method according to any one of claims 4 to 7.
CN202310045633.3A 2023-01-30 2023-01-30 High-toughness alloy forged steel for high-speed rail brake disc with speed of 400 km per hour, heat treatment method and production method thereof Active CN116043114B (en)

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Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2009149922A (en) * 2007-12-19 2009-07-09 Sumitomo Metal Ind Ltd Steel material for brake disc, and brake disc
CN102953008A (en) * 2011-08-25 2013-03-06 南车戚墅堰机车车辆工艺研究所有限公司 Alloy forged steel and its heat treatment method and use
CN103510024A (en) * 2012-06-28 2014-01-15 南车戚墅堰机车车辆工艺研究所有限公司 Alloy cast steel for high speed train brake disc, heat treatment method thereof and high speed train brake disc manufactured by the alloy cast steel
CN106967929A (en) * 2017-03-28 2017-07-21 马钢(集团)控股有限公司 A kind of EMUs brake disc forging mild steel and its heat treatment method
JP2017128795A (en) * 2016-01-18 2017-07-27 株式会社神戸製鋼所 Steel for forging and large sized forged steel article
JP2020059881A (en) * 2018-10-09 2020-04-16 日本製鉄株式会社 Steel material and method for manufacturing the same

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2009149922A (en) * 2007-12-19 2009-07-09 Sumitomo Metal Ind Ltd Steel material for brake disc, and brake disc
CN102953008A (en) * 2011-08-25 2013-03-06 南车戚墅堰机车车辆工艺研究所有限公司 Alloy forged steel and its heat treatment method and use
CN103510024A (en) * 2012-06-28 2014-01-15 南车戚墅堰机车车辆工艺研究所有限公司 Alloy cast steel for high speed train brake disc, heat treatment method thereof and high speed train brake disc manufactured by the alloy cast steel
JP2017128795A (en) * 2016-01-18 2017-07-27 株式会社神戸製鋼所 Steel for forging and large sized forged steel article
CN106967929A (en) * 2017-03-28 2017-07-21 马钢(集团)控股有限公司 A kind of EMUs brake disc forging mild steel and its heat treatment method
JP2020059881A (en) * 2018-10-09 2020-04-16 日本製鉄株式会社 Steel material and method for manufacturing the same

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