CN107760838A - A kind of brake disc of high-speed train Heat-Treatment of Steel method - Google Patents
A kind of brake disc of high-speed train Heat-Treatment of Steel method Download PDFInfo
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- CN107760838A CN107760838A CN201711041248.2A CN201711041248A CN107760838A CN 107760838 A CN107760838 A CN 107760838A CN 201711041248 A CN201711041248 A CN 201711041248A CN 107760838 A CN107760838 A CN 107760838A
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/28—Normalising
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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
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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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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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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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- 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
- C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
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Abstract
The invention discloses a kind of brake disc of high-speed train Heat-Treatment of Steel method, including normalizing, quenching and tempering process, the heating-up temperature of three is respectively 1000~1100 DEG C, 980~1020 DEG C and 980~1020 DEG C, and time of insulation is respectively 3.75~6.00min/mm, 3.00~4.50min/mm, 3.75~6.00min/mm by the thickness gauge of steel.The crystallite dimension of the brake disc of high-speed train steel obtained in this way is 20~25 μm, carbide average grain diameter is between 0.020 μm~0.040 μm, it is organized as tempered sorbite, with excellent high-temperature behavior, it is 35~40W/ (mK) in 20 DEG C~700 DEG C of thermal conductivity factors, 500 DEG C of tensile strength >=1000MPa, 600 DEG C of tensile strength >=900Mpa, produced through 20 DEG C~700 DEG C cold cyclings, 1000 flawlesses.
Description
Technical field
The invention belongs to high-speed rail transportation parts steel technical field, and in particular to a kind of brake disc of high-speed train is used
Heat-Treatment of Steel method.
Background technology
With the raising of bullet train speed, promptness, safety and stability to train braking propose higher
It is required that this also means that the quality and performance of train braking device and brake material are needed to meet higher requirement.Arrange at a high speed
Car foundation brake uses disc brake, is usually to be braked using forged steel in the world for more than 200km/h bullet trains
Disk and the brake apparatus of powder metallurgy brake pad pairing.Its most basic function of brake disc is to absorb braking kinetic energy and be converted into it
Heat energy is dispersed into air.
The high-temperature behavior for improving Materials for High-speed Train Brake Discs is to lift the most key technology of brake apparatus reliability to ask
One of topic.Under bullet train speed height and the severe damped condition of service condition, huge braking thermic load and thermal shock meeting
Bring very high thermal stress and thermograde.Therefore disc material must have good mechanical behavior under high temperature and thermal conductivity
Can, and low elastic modulus and low thermal coefficient of expansion so that braking heat can rapid loss.Specifically, high-speed train braking
Disk should have following performance：First, stable and uniform frictional behaviour, coefficient of friction is not with the change of pressure, temperature and speed
Change and change；Second, good fatigue performance and fabulous heat resistanceheat resistant crackle extended capability, to reduce brake disc friction surface urgency
Damage of the high thermal stress that cold anxious heat is formed to brake disc；Third, higher anti-wear performance, is produced with reducing card friction
Abrasion；Disc material should also have good friction resistant thermal deformation behavior and thermal conductivity.
Current research is largely focused on innovation brake disc structure, in terms of improving brake disc thermal diffusivity, to the wound of material
New Journal of Sex Research is relatively fewer.And in train braking, particularly brake hard when, the instantaneous thermal energy of brake disc is difficult quick release
Go out, therefore, the high-temperature behavior for improving disc material is significant to improving the brake disc life-span.
The content of the invention
Based on above-mentioned background, the invention provides a kind of brake disc of high-speed train steel, and it has excellent high-temperature behavior.
Brake disc of high-speed train disclosed by the invention " bullet train " described in steel refers to that speed per hour arranges at a high speed in more than 200km/h
Car.
The technical scheme that the present invention takes is：
A kind of brake disc of high-speed train Heat-Treatment of Steel method, the heat treatment method comprise the following steps：
(1) normalizing process：Brake disc of high-speed train is heated to 1000~1100 DEG C with steel, 300 DEG C are air-cooled to after insulation
Below；
(2) quenching technical：Brake disc of high-speed train after normalizing is heated to 980~1020 DEG C with steel, water after insulation
It is cooled to less than 100 DEG C；
(3) tempering process：Brake disc of high-speed train after quenching is heated to 600~650 DEG C with steel, water cooling after insulation
To less than 100 DEG C.
Further, the heat treatment method preferably includes following steps：
(1) normalizing process：Brake disc of high-speed train is heated to 1040~1070 DEG C with steel, 300 DEG C are air-cooled to after insulation
Below；
(2) quenching technical：Brake disc of high-speed train after normalizing is heated to 1000~1015 DEG C with steel, water after insulation
It is cooled to less than 100 DEG C；
(3) tempering process：Brake disc of high-speed train after quenching is heated to 620~640 DEG C with steel, water cooling after insulation
To less than 100 DEG C.
In heat treatment process, the temperature in normalizing and quenching process is controlled in 1000~1100 DEG C and 980- respectively
1020 DEG C, soaking time controls 5~8 hours and 4~6 hours respectively.On the one hand the full and uniform dissolving of all elements is ensured
In high temperature austenite, it is ready for the uniformity of tissue and composition after quenching；On the other hand, the Ovshinsky of appropriate size is ensured
Body grain size, if grain size is bigger than normal, thick, the high-temperature behavior reduction of steel was organized, and if grain size is meticulous, it is big in tissue
Angle grain boundary improves, and reduces the thermal conductivity of steel.600-650 DEG C optimal of temperature range of age hardening effect is selected in drawing process
It is tempered, the carbide in steel is fully separated out, and ensure that carbide size is moderate, both can guarantee that the high-temperature behavior of steel, also
Steel structure stability during rapid heat cycle can be improved, improves the thermal conductivity factor of steel under the high temperature conditions.
In the normalizing process, the speed of heating is 50~100 DEG C/h；The time of insulation is calculated as 3.75 by the thickness of steel~
6.00min/mm。
In the quenching technical, the speed of heating is 50~100 DEG C/h, time of insulation is calculated as 3.00 by the thickness of steel~
4.50min/mm。
In the tempering process, the speed of heating is 50~100 DEG C/h；The time of insulation is calculated as 3.75 by the thickness of steel~
6.00min/mm。
The speed of heating is controlled in 50~100 DEG C/h in normalizing, quenching and tempering process, its reason is to add
Hot speed is too fast to be also easy to produce crackle, and the rate of heat addition is too slow, and the efficiency of heating surface reduces.
The brake disc of high-speed train includes following composition and percentage by weight with ladle：C：0.20~0.30%, Si：0.20
~0.40%0, Mn：0.20~0.40%, Cr：0.90~1.50%, W：0.30~0.60%, Mo：0.40~0.90%, Al：
≤ 0.025%, V：0.70~1.00%, Co：0.20~0.40%, Ni：≤ 0.20%, Cu：≤ 0.20%, N：≤ 0.005%,
P≤0.010%, S≤0.005%, surplus are Fe and inevitable impurity；And meet 0.9C≤0.03W+0.063Mo+
0.06Cr+0.2V≤1.1C。
Preferably, C：0.26~0.29%, Si：0.22~0.28%, Mn：0.22~0.31%, Cr：0.93~1.0%,
W：0.33~0.38%, Mo：0.75~0.88%, Al：≤ 0.018%, V：0.92~1.00%, Co：0.22~0.29%,
Ni：≤ 0.16%, Cu：≤ 0.18%, N：≤ 0.003%, P≤0.008%, S≤0.001%, surplus is for Fe and unavoidably
Impurity；And meet 0.9C≤0.03W+0.063Mo+0.06Cr+0.2V≤1.1C.
On the Design of Chemical Composition of steel, reduce as far as possible and expand γ phases p-block element p (C, N, Mn, Ni, Cu) content, improve contracting
The content of small γ phases p-block element p (W, Mo, Cr, V), the V content in steel is especially improved, ensure the stabilization of carbide after heat treatment
Property, and certain content Co is properly added, age hardening effect of the increase steel in drawing process.The effect of each chemical element and set
Meter is as follows：
C：C element is necessary to obtaining high intensity, hardness.Although high C content has to the intensity of steel, hardness etc.
Profit, but it is totally unfavorable to the plasticity and toughness of steel, and reduce yield tensile ratio, Decarburization Sensitivity increase, deteriorate the fatigue resistance of steel
Energy, processing characteristics and high-temp plastic.Therefore the appropriate C content reduced in steel, is controlled below 0.30%.However, quenching
With after high tempering in order to obtain required high intensity, C content must more than 0.20%, thus C content preferably control as 0.20~
0.30%.
Si：Si is deoxidant element main in steel, has very strong solution strengthening effect, but Si too high levels will make steel
Plasticity and toughness decline, C activity increase, promote decarburization and graphitization tendency of the steel in rolling and heat treatment process, and
Make smelting difficult and easily form field trash, deteriorate the anti-fatigue performance of steel.Therefore it is 0.20~0.40% to control Si contents.
Mn：Mn is the effective element of deoxidation and desulfurization, can also improve the quenching degree and intensity of steel.But quench temper
When, Mn and P have strong grain boundary cosegregation tendency, promote temper brittleness, deteriorate the toughness of steel, cross high Mn content and be easily caused repeatedly
Heat and austeno-martensite transformation is produced in cooling procedure, cause thermal coefficient of expansion, thermal conductivity factor violent change, it is cold to reduce brake disc
Thermal fatigue property, thus Mn contents are controlled 0.20%~0.40%.
V：V is strong carbide element, and strong diminution γ phase p-block element ps, has strong age hardening effect, improves steel
High-temperature behavior, while can also improve and heat the stability organized in cooling procedure repeatedly, therefore, control V content as 0.70
~1.00%.
Cr：Cr can effectively improve the quenching degree and resistance to tempering of steel, to obtain required high intensity；Cr may be used also simultaneously
C activity is reduced, the steel surface decarburizing tendency in heating, rolling and heat treatment process can be reduced, has utilization to obtain high resist
Fatigue behaviour and good high-temperature behavior.But too high levels can deteriorate the toughness of steel, thus control Cr contents for 0.90~
1.50%.
Mo：Effects of the Mo in steel predominantly improves quenching degree, improves resistance to tempering and prevent temper brittleness.In addition, Mo
The reasonable cooperation of element and Cr elements can make quenching degree and resistance to tempering be improved significantly, and Mo contents are too low, and above-mentioned effect has
Limit, Mo too high levels, then above-mentioned effect saturation, and improve the cost of steel.Therefore, it is 0.40~0.90% to control Mo contents.
W：W is carbide, improves the elevated temperature strength and heat resistance of steel, considering cost factor, and W contains
Amount should be controlled 0.30~0.60%.
Co：Although Co is to expand γ phase p-block element ps, but appropriate Co can effectively facilitate the precipitation of alloy carbide, increase it
The spread, age hardening effect is improved, therefore, Co contents should be controlled 0.20~0.40%.
Al：Al is deoxidant element main in steel, and forming AlN precipitated phases with N element in steel, there is suppression crystal grain to grow up, but
Crossing fine grain causes high-temperature behavior to reduce, and therefore, Al content should be controlled≤0.025%.
Ni：Ni can improve the quenching degree of steel, the toughness of corrosion resistance and guarantee steel at low temperature.But too high Ni contents are easily caused
Heat repeatedly in cooling procedure and produce austeno-martensite transformation, cause thermal coefficient of expansion violent change, reduce brake disc cool-hot fatigue
Performance, therefore Ni contents are≤0.20%.
Cu：Precipitation strength is realized by separating out ε-Cu, improves the intensity of steel, in addition, adding appropriate Cu elements, additionally it is possible to
Increase the atmospheric corrosion resistance of steel, but Cu is to expand γ phase p-block element ps, and the higher brake disc that is easily caused of content heats cooling repeatedly
During produce austeno-martensite transformation, cause thermal coefficient of expansion violent change, reduce brake disc cold-heat fatigue property, therefore, Cu
Content should be controlled≤0.20%.
P：Microsegregation is formed in solidification of molten steel, segregation makes steel to crystal boundary when then temperature heats after austenite
Fragility significantly increases, so that the temper brittleness tendency increase of steel.Therefore, P content should be controlled below 0.010%.
S：Inevitable impurity, form MnS field trashes and can deteriorate the toughness of steel in cyrystal boundary segregation, so as to reduce steel
Toughness plasticity.Because Mn contents are relatively low in steel, therefore, S contents should be controlled below 0.005%.
N：The precipitation of carbon VN, AlN in austenite is promoted containing too high N content in V, Al steel, fining austenite grains simultaneously drop
Low steel belt roof bolt drag, therefore, N content should be controlled in≤60ppm
The invention also discloses the brake disc of high-speed train steel obtained according to above-mentioned heat treatment method.
The crystallite dimension of the brake disc of high-speed train steel be 20~25 μm, carbide average grain diameter 0.020 μm~
Between 0.040 μm, tempered sorbite is organized as.
The brake disc of high-speed train steel is 35~40W/ (mK) in 20 DEG C~700 DEG C of thermal conductivity factor, and 500 DEG C anti-
Tensile strength >=1000MPa, 600 DEG C of tensile strength >=900MPa, produced through 20 DEG C~700 DEG C cold cyclings, 1000 flawlesses.
Compared with prior art, brake disc of high-speed train steel disclosed by the invention and common forging brake disc steel phase
Than while there is excellent high temperature intensity, also with excellent thermal conductivity factor, so as to significantly improve the military service performance of brake disc.
Embodiment
Embodiment 1
A kind of brake disc of high-speed train Heat-Treatment of Steel method, comprises the following steps：
(1) normalizing process：Brake disc of high-speed train is heated to 1100 DEG C with 53 DEG C/h firing rate with steel, is incubated 5h
After be air-cooled to less than 300 DEG C；
(2) quenching technical：Brake disc of high-speed train after normalizing is heated to steel with 53 DEG C/h firing rate
1020 DEG C, water cooling is to less than 100 DEG C after being incubated 4h；
(3) tempering process：Brake disc of high-speed train after quenching is heated to 650 with steel with 53 DEG C/h firing rate
DEG C, after insulation after 5h water cooling to less than 100 DEG C.
The preparation technology of brake disc of high-speed train steel is as follows：Electric arc furnaces or converter smelting → LF stoves refining → RH or VD are true
Empty degassing → continuous casting → heating strand stove heat → brake disc round rolling → brake disc blank forging → heat treatment → machine adds
Work → flaw detection；It is heated to be rolled intoRound steel, then heated it is forged into brake disc blank, maximum gauge 80mm.
And mechanical behavior under high temperature and thermal conductivity factor analysis, its high-temperature mechanics are carried out with steel to last brake disc of high-speed train
The analysis result of performance is shown in Table 2, and thermal conductivity factor analysis result is shown in Table 3.
Shown in embodiment 1 in chemical composition and the weight percent such as table 1 of the brake disc of high-speed train steel：
The chemical composition and percentage by weight of the high speed train brake disk steel of 1 embodiment of table 1~4
Embodiment 2
A kind of brake disc of high-speed train Heat-Treatment of Steel method, comprises the following steps：
(1) normalizing process：Brake disc of high-speed train is heated to 1070 DEG C with 66 DEG C/h firing rate with steel, is incubated 6h
After be air-cooled to less than 300 DEG C；
(2) quenching technical：Brake disc of high-speed train after normalizing is heated to steel with 66 DEG C/h firing rate
1015 DEG C, water cooling is to less than 100 DEG C after being incubated 4.5h；
(3) tempering process：Brake disc of high-speed train after quenching is heated to 640 with steel with 66 DEG C/h firing rate
DEG C, after insulation after 6h water cooling to less than 100 DEG C.
The preparation technology of brake disc of high-speed train steel is as follows：Electric arc furnaces or converter smelting → LF stoves refining → RH or VD are true
Empty degassing → continuous casting → heating strand stove heat → brake disc round rolling → brake disc blank forging → heat treatment → machine adds
Work → flaw detection；It is heated to be rolled intoRound steel, then heated it is forged into brake disc blank, thickness 65mm.
And mechanical behavior under high temperature and thermal conductivity factor analysis, its high-temperature mechanics are carried out with steel to last brake disc of high-speed train
The analysis result of performance is shown in Table 2, and thermal conductivity factor analysis result is shown in Table 3.
The chemical composition and percentage by weight of the brake disc of high-speed train steel are as shown in table 1, embodiment 2.
Embodiment 3
A kind of brake disc of high-speed train Heat-Treatment of Steel method, comprises the following steps：
(1) normalizing process：Brake disc of high-speed train is heated to 1040 DEG C with steel with 78 DEG C/h firing rate, insulation
Less than 300 DEG C are air-cooled to after 6.5h；
(2) quenching technical：Brake disc of high-speed train after normalizing is heated to steel with 78 DEG C/h firing rate
1000 DEG C, water cooling is to less than 100 DEG C after being incubated 4.8h；
(3) tempering process：Brake disc of high-speed train after quenching is heated to 620 with steel with 78 DEG C/h firing rate
DEG C, after insulation after 6.5h water cooling to less than 100 DEG C.
The preparation technology of brake disc of high-speed train steel is as follows：Electric arc furnaces or converter smelting → LF stoves refining → RH or VD are true
Empty degassing → continuous casting → heating strand stove heat → brake disc round rolling → brake disc blank forging → heat treatment → machine adds
Work → flaw detection；It is heated to be rolled intoRound steel, then heated it is forged into brake disc blank, thickness 65mm.
And mechanical behavior under high temperature and thermal conductivity factor analysis, its high-temperature mechanics are carried out with steel to last brake disc of high-speed train
The analysis result of performance is shown in Table 2, and thermal conductivity factor analysis result is shown in Table 3.
Shown in embodiment 3 in chemical composition and the weight percent such as table 1 of the brake disc of high-speed train steel.
Embodiment 4
A kind of brake disc of high-speed train Heat-Treatment of Steel method, comprises the following steps：
(1) normalizing process：Brake disc of high-speed train is heated to 1000 DEG C with 98 DEG C/h firing rate with steel, is incubated 8h
After be air-cooled to less than 300 DEG C；
(2) quenching technical：Brake disc of high-speed train after normalizing is heated to 980 with steel with 98 DEG C/h firing rate
DEG C, water cooling is to less than 100 DEG C after being incubated 6h；
(3) tempering process：Brake disc of high-speed train after quenching is heated to 600 with steel with 98 DEG C/h firing rate
DEG C, after insulation after 8h water cooling to less than 100 DEG C.
The preparation technology of brake disc of high-speed train steel is as follows：Electric arc furnaces or converter smelting → LF stoves refining → RH or VD are true
Empty degassing → continuous casting → heating strand stove heat → brake disc round rolling → brake disc blank forging → heat treatment → machine adds
Work → flaw detection；It is heated to be rolled intoRound steel, then heated it is forged into brake disc blank, maximum gauge 80mm.
And mechanical behavior under high temperature and thermal conductivity factor analysis, its high-temperature mechanics are carried out with steel to last brake disc of high-speed train
The analysis result of performance is shown in Table 2, and thermal conductivity factor analysis result is shown in Table 3.
Shown in embodiment 4 in chemical composition and the weight percent such as table 1 of the brake disc of high-speed train steel.
Table 2 embodiment 1-4 brake disc of high-speed train Heat-Treatment of Steel technique and mechanical behavior under high temperature
Thermal conductivity factor of the embodiment 1-4 brake disc of high-speed train of table 3 with steel at different temperatures
The brake disc of high-speed train that various embodiments above obtains is 20~25 μm with the crystallite dimension of steel, and carbide is average
Particle diameter is between 0.020 μm~0.040 μm, and tissue is tempered sorbite, 20 DEG C~700 DEG C 35~40W/ of thermal conductivity factor (m
K), 500 DEG C of tensile strength >=1000MPa, 600 DEG C of tensile strength >=900MPa, through 20 DEG C~700 DEG C cold cyclings, 1000 nothings
Crackle produces.
If change the parameter in the content or Technology for Heating Processing of the chemical composition of brake disc of high-speed train steel at this
Outside invention, then the goal of the invention of the present invention, the crystallite dimension crystal grain chi of obtained brake disc of high-speed train steel can not be realized
Very little to be less than 20 μm or more than 25 μm, for carbide average grain diameter between 0.060 μm~0.080 μm, tissue is tempered sorbite,
There is crackle generation 1000 times through 20 DEG C~700 DEG C cold cyclings.It can be seen that if chemical composition by brake disc of high-speed train steel
Or the parameter setting in Technology for Heating Processing is outside scope disclosed by the invention, the height of obtained brake disc of high-speed train steel
Warm nature can be more of the invention far short of what is expected.
A kind of above-mentioned detailed description carried out with reference to embodiment to brake disc of high-speed train with Heat-Treatment of Steel method, is to say
It is bright property rather than limited, several embodiments can be included according to limited scope, therefore it is of the invention total not departing from
Changing and modifications under body design, should belong within protection scope of the present invention.
Claims (10)
1. a kind of brake disc of high-speed train Heat-Treatment of Steel method, it is characterised in that the heat treatment method includes following step
Suddenly：
(1) normalizing process：Brake disc of high-speed train is heated to 1000~1100 DEG C with steel, less than 300 DEG C are air-cooled to after insulation；
(2) quenching technical：Brake disc of high-speed train after normalizing is heated to 980~1020 DEG C with steel, water cooling is extremely after insulation
Less than 100 DEG C；
(3) tempering process：Brake disc of high-speed train after quenching is heated to 600~650 DEG C with steel, water cooling is extremely after insulation
Less than 100 DEG C.
2. heat treatment method according to claim 1, it is characterised in that the heat treatment method comprises the following steps：
(1) normalizing process：Brake disc of high-speed train is heated to 1040~1070 DEG C with steel, less than 300 DEG C are air-cooled to after insulation；
(2) quenching technical：Brake disc of high-speed train after normalizing is heated to 1000~1015 DEG C with steel, water cooling is extremely after insulation
Less than 100 DEG C；
(3) tempering process：Brake disc of high-speed train after quenching is heated to 620~640 DEG C with steel, water cooling is extremely after insulation
Less than 100 DEG C.
3. according to the heat treatment method described in any one of claim 1 or 2, it is characterised in that in the normalizing process, heating
Speed be 50~100 DEG C/h；The time of insulation is calculated as 3.75~6.00min/mm by the thickness of steel.
4. according to the heat treatment method described in claim 1-3 any one, it is characterised in that in the quenching technical, heating
Speed be 50~100 DEG C/h, the time of insulation is calculated as 3.00~4.50min/mm by the thickness of steel.
5. according to the heat treatment method described in claim 1-4 any one, it is characterised in that in the tempering process, heating
Speed be 50~100 DEG C/h；The time of insulation is calculated as 3.75~6.00min/mm by the thickness of steel.
6. according to the heat treatment method described in claim 1-5 any one, it is characterised in that the brake disc of high-speed train is used
Ladle includes following composition and percentage by weight：C：0.20~0.30%, Si：0.20~0.40%0, Mn：0.20~0.40%,
Cr：0.90~1.50%, W：0.30~0.60%, Mo：0.40~0.90%, Al：≤ 0.025%, V：0.70~1.00%,
Co：0.20~0.40%, Ni：≤ 0.20%, Cu：≤ 0.20%, N：≤ 0.005%, P≤0.010%, S≤0.005% are remaining
Measure as Fe and inevitable impurity；And meet 0.9C≤0.03W+0.063Mo+0.06Cr+0.2V≤1.1C.
7. heat treatment method according to claim 6, it is characterised in that the brake disc of high-speed train is included as follows with ladle
Composition and percentage by weight：C：0.26~0.29%, Si：0.22~0.28%, Mn：0.22~0.31%, Cr：0.93~
1.0%, W：0.33~0.38%, Mo：0.75~0.88%, Al：≤ 0.018%, V：0.92~1.00%, Co：0.22~
0.29%, Ni：≤ 0.16%, Cu：≤ 0.18%, N：≤ 0.003%, P≤0.008%, S≤0.001%, surplus is for Fe and not
Evitable impurity；And meet 0.9C≤0.03W+0.063Mo+0.06Cr+0.2V≤1.1C.
8. the brake disc of high-speed train steel that the heat treatment method according to claim 1-7 any one obtains.
9. brake disc of high-speed train steel according to claim 8, it is characterised in that the brake disc of high-speed train steel
Crystallite dimension be 20~25 μm, carbide average grain diameter is organized as tempered sorbite between 0.020 μm~0.040 μm.
10. brake disc of high-speed train steel according to claim 8, it is characterised in that the brake disc of high-speed train is used
Steel is 35~40W/ (mK) in 20 DEG C~700 DEG C of thermal conductivity factor, 500 DEG C of tensile strength >=1000MPa, and 600 DEG C of tensions are strong
Degree >=900MPa, produced through 20 DEG C~700 DEG C cold cyclings, 1000 flawlesses.
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| CN112322864A (en) * | 2020-11-05 | 2021-02-05 | 盐城市明佳机械有限公司 | Precision forging forming process of 270 MPa-level clutch for electric vehicle |
| CN116043115A (en) * | 2023-01-31 | 2023-05-02 | 马鞍山钢铁股份有限公司 | Cold and hot fatigue resistant forged steel for high-speed railway brake disc and heat treatment method and production method thereof |
| CN116043115B (en) * | 2023-01-31 | 2024-05-14 | 马鞍山钢铁股份有限公司 | Cold and hot fatigue resistant forged steel for high-speed railway brake disc and heat treatment method and production method thereof |
| RU2816975C1 (en) * | 2023-06-15 | 2024-04-08 | Федеральное государственное бюджетное учреждение науки Хабаровский Федеральный исследовательский центр Дальневосточного отделения Российской академии наук | Method of heat treatment of articles made from steel with carbon content of 0,4-1,5% |
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