CN107746915B - A kind of brake disc of high-speed train steel - Google Patents
A kind of brake disc of high-speed train steel Download PDFInfo
- Publication number
- CN107746915B CN107746915B CN201711033158.9A CN201711033158A CN107746915B CN 107746915 B CN107746915 B CN 107746915B CN 201711033158 A CN201711033158 A CN 201711033158A CN 107746915 B CN107746915 B CN 107746915B
- Authority
- CN
- China
- Prior art keywords
- brake disc
- speed train
- steel
- train steel
- tempering
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Classifications
-
- 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
-
- 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
-
- 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
-
- 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
-
- 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
-
- 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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- 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
-
- 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
- C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
-
- 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
-
- 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
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- 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
-
- 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
- C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
Abstract
The invention discloses a kind of brake disc of high-speed train steel, including following chemical component and mass percent: 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 :≤0.0050%, 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.It is 35~40W/ (mK), 500 DEG C of tensile strength >=1000MPa, 600 DEG C of tensile strength >=900MPa with excellent high-temperature behavior, 20 DEG C~700 DEG C thermal coefficients.
Description
Technical field
The invention belongs to high-speed rail transportation components steel technical fields, and in particular to a kind of brake disc of high-speed train use
Steel.
Background technique
With the raising of bullet train speed, the timeliness of train braking, safety and stability are proposed higher
It is required that this also means that quality and performance to train braking device and brake material need to meet higher requirement.High speed arranges
Vehicle foundation brake is all made of disc brake, and for 200km/h or more bullet train, forged steel braking is usually used in the world
The brake apparatus of disk and powder metallurgy brake pad pairing.Its most basic function of brake disc is to absorb braking kinetic energy and convert it to
Thermal energy is dispersed into air.
The high-temperature behavior for improving Materials for High-speed Train Brake Discs is to promote the most key technology of brake apparatus reliability to ask
One of topic.Under the severe damped condition of bullet train speed height and service condition, huge braking thermic load and thermal shock meeting
Bring very high thermal stress and temperature gradient.Therefore disc material must have good mechanical behavior under high temperature and thermal conductivity
Energy and low elastic modulus and low thermal coefficient of expansion, enable and brake the rapid loss of heat.In particular, high-speed train braking
Disk should have following performance: first is that stable and uniform frictional behaviour, coefficient of friction is not with the change of pressure, temperature and speed
Change and changes；Second is that good fatigue performance and fabulous heat resistanceheat resistant crackle extended capability, anxious to reduce brake disc friction surface
Cold urgency heat is formed by damage of the high thermal stress to brake disc；Third is that higher wear-resisting property, is generated with reducing disk friction
Abrasion；Disc material should also have good anti-friction 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, especially emergency braking when, the instantaneous thermal energy of brake disc is difficult quick release
It goes out, therefore, the high-temperature behavior for improving disc material is of great significance to the brake disc service life is improved.
Summary of the invention
Based on the above background, the present invention provides a kind of brake disc of high-speed train steel, with excellent high-temperature behavior.
The technical scheme adopted by the invention is as follows:
A kind of brake disc of high-speed train steel, including following chemical component and mass percent: 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:
≤ 0.0050%, 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:0.26~0.28%, Si:0.30~0.35%, Mn:0.32~0.35%, Cr:1.08~
1.38%, W:0.40~0.50%, Mo:0.58~0.73%, Al :≤0.025%, V:0.75~0.90%, Co:0.30~
0.35%, Ni :≤0.18%, Cu :≤0.20%, N :≤0.0050%, P≤0.009%, S≤0.002%, surplus be Fe and
Inevitable impurity；And meet 0.9C≤0.03W+0.063Mo+0.06Cr+0.2V≤1.1C.
The crystallite dimension of the brake disc of high-speed train steel be 20~25 μm, carbide average grain diameter 0.020 μm~
It between 0.040 μm, organizes as tempered sorbite, 20 DEG C~700 DEG C thermal coefficients are 35~40W/ (mK), and 500 DEG C of tensions are strong
Degree >=1000MPa, 600 DEG C of tensile strength >=900MPa.
The preparation method of the brake disc of high-speed train steel includes following technique: electric arc furnaces or converter smelting → LF furnace essence
Refining → RH or VD vacuum outgas → continuous casting → slab heating stove heating → brake disc with round rolling → brake disc blank forging →
Normalizing+Tempering and Quenching → machining → flaw detection.
Normalizing+the quenching-and-tempering process includes normalizing process, quenching technical and tempering process.
In the normalizing process, normalizing temperature is 1000~1100 DEG C, soaking time 5~8 hours.
In the quenching technical, hardening heat be 980~1020 DEG C, soaking time 4~6 hours, hardening media be 5%~
The PAG quenching liquid of 12% mass concentration.
In the tempering process, tempering temperature is 600~650 DEG C, and soaking time is 5~8 hours.
Further include after normalizing process it is air-cooled, be air-cooled to 300 DEG C or less, it is ensured that tissue sufficiently transformation, and ensure refine crystal grain
The second phase be sufficiently precipitated in cooling procedure and keep smaller size.
It further include water cooling after tempering process, water cooling is to 100 DEG C hereinafter, reducing the temper brittleness area residence time to the greatest extent.
Brake disc of high-speed train disclosed by the invention " bullet train " described in steel refer to speed per hour 200km/h with
Upper bullet train, the present invention have obtained having tempering by the control to chemical element content contained by steel and heat treatment process
The brake disc of high-speed train steel of Soxhlet body tissue, with excellent high-temperature behavior, and through 20 DEG C~700 DEG C cold cyclings
1000 times flawless generates.
It on the Design of Chemical Composition of steel, reduces expand γ phase p-block element p (C, N, Mn, Ni, Cu) content as far as possible, improve contracting
V content in the content of small γ phase p-block element p (W, Mo, Cr, V), especially raising steel, guarantees the stabilization of carbide after heat treatment
Property, and it is properly added certain content Co, increase age hardening effect of the steel in drawing process.It the effect of each chemical element and sets
It counts as follows:
C:C element is necessary to obtaining high intensity, hardness.Although high C content has intensity, the hardness etc. of steel
Benefit, 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 performance and high-temp plastic.Therefore the appropriate C content reduced in steel, is controlled below 0.30%.However, quenching
With obtain required high intensity after high tempering, C content must 0.20% or more, thus C content preferably control as 0.20~
0.30%.
Si:Si is main deoxidant element in steel, has very strong solution strengthening effect, but Si too high levels will make steel
Plasticity and toughness decline, the activity of C increase, and promote decarburization and graphitization tendency of the steel in rolling and heat treatment process, and
Make to smelt difficult and easily form field trash, deteriorates the anti-fatigue performance of steel.Therefore control Si content is 0.20~0.40%.
Mn:Mn is the effective element of deoxidation and desulfurization, can also improve the harden ability and intensity of steel.But quench steel tempering
When, Mn and P have strong grain boundary cosegregation tendency, promote temper brittleness, deteriorate the toughness of steel, cross high Mn content and easily lead to repeatedly
It heats and generates austeno-martensite transformation in cooling procedure, lead to thermal expansion coefficient, thermal coefficient violent change, it is cold to reduce brake disc
Thermal fatigue property, thus Mn content is controlled 0.20%~0.40%.
V:V is strong carbide element and strong diminution γ phase p-block element p, 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 is 0.70
~1.00%.
Cr:Cr can effectively improve the harden ability and resistance to tempering of steel, to obtain required high intensity；Cr may be used also simultaneously
The activity for reducing C, can reduce the steel surface decarburizing tendency in heating, rolling and heat treatment process, have and resist using acquisition is high
Fatigue behaviour and good high-temperature behavior.But too high levels can deteriorate the toughness of steel, thus control Cr content be 0.90~
1.50%.
Effect of the Mo:Mo in steel predominantly improves harden ability, improves resistance to tempering and prevent temper brittleness.In addition, Mo
The reasonable cooperation of element and Cr element can make harden ability and resistance to tempering be improved significantly, and Mo content is too low, and above-mentioned effect has
Limit, Mo too high levels, then above-mentioned effect saturation, and the cost of raising steel.Therefore, control Mo content is 0.40~0.90%.
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%.
Although Co:Co is to expand γ phase p-block element p, but Co appropriate can effectively facilitate the precipitation of alloy carbide, increase it
The spread improves age hardening effect, and therefore, Co content should be controlled 0.20~0.40%.
Al:Al is main deoxidant element in steel, and forming AlN precipitated phase with N element in steel, there is inhibition crystal grain to grow up, but
Crossing fine grain causes high-temperature behavior to reduce, and therefore, Al content should be controlled≤0.025%.
The harden ability of steel, the toughness of corrosion resistance and guarantee steel at low temperature can be improved in Ni:Ni.But excessively high Ni content is easily led to
It is heated in cooling procedure repeatedly and generates austeno-martensite transformation, lead to thermal expansion coefficient violent change, reduce brake disc cool-hot fatigue
Performance, therefore Ni content is≤0.20%.
Cu: precipitation strength is realized by the way that ε-Cu is precipitated, the intensity of steel is improved, in addition, suitable Cu element is added, additionally it is possible to
Increase the atmospheric corrosion resistance of steel, but Cu is to expand γ phase p-block element p, the higher brake disc that easily leads to of content heats cooling repeatedly
Austeno-martensite transformation is generated in the process, leads to thermal expansion coefficient violent change, reduces brake disc cold-heat fatigue property, therefore, Cu
Content should be controlled≤0.20%.
P: forming microsegregation in solidification of molten steel, and segregation makes steel to crystal boundary when then temperature heats after austenite
Brittleness significantly increases, and increases so that the temper brittleness of steel be made to be inclined to.Therefore, P content should control below 0.010%.
S: inevitable impurity forms MnS field trash and can deteriorate the toughness of steel in cyrystal boundary segregation, to reduce steel
Toughness plasticity.Since Mn content is lower in steel, S content should control below 0.005%.
N: carbon VN, AlN are promoted in the precipitation of austenite containing N content excessively high in V, Al steel, fining austenite grains simultaneously drop
Low steel belt roof bolt drag, therefore, N content should be controlled in≤60ppm.
During heat treatment, the temperature in normalizing and quenching process is controlled respectively in 1000~1100 DEG C and 980-
1020 DEG C, soaking time is controlled respectively 5~8 hours and 4~6 hours, on the one hand guarantees the full and uniform dissolution of all elements
In high temperature austenite, it is ready for the uniformity of tissue and ingredient after quenching；On the other hand, guarantee the Ovshinsky of appropriate size
Body grain size organized thick, the high-temperature behavior reduction of steel if grain size is bigger than normal, and if grain size is meticulous, it is big in tissue
Angle grain boundary improves, and reduces the thermal conductivity of steel.Optimal 600-650 DEG C of temperature range of age hardening effect is selected in drawing process
It being tempered, tempering insulation time is 5~8 hours, the carbide in steel is precipitated sufficiently, and guarantee that carbide size is moderate,
Both the high-temperature behavior of steel had been can guarantee, additionally it is possible to improve steel structure stability during rapid heat cycle, improve steel in hot conditions
Under thermal coefficient.
Compared with prior art, brake disc of high-speed train steel disclosed by the invention and common forging brake disc steel phase
Than also there is excellent thermal coefficient, to significantly improve the military service performance of brake disc while there is excellent high temperature intensity.
Specific embodiment
Examples 1 to 4
A kind of brake disc of high-speed train steel, chemical component and weight percent are as shown in table 1:
The chemical component and weight percent of 1 Examples 1 to 4 high speed train brake disk steel of table
The preparation method of the brake disc of high-speed train steel includes following technique: electric arc furnaces or converter smelting → LF furnace essence
Refining → RH or VD vacuum outgas → continuous casting → slab heating stove heating → brake disc with round rolling → brake disc blank forging →
Normalizing+Tempering and Quenching → machining → flaw detection.It is heated to be rolled intoRound steel, then heated it is forged into brake disc
Blank carries out mechanical behavior under high temperature after table 2 is heat-treated, is finish-machined to drawing by high temperature and thermal coefficient sample with a thickness of 65mm
It is analyzed with thermal coefficient, the analysis of mechanical behavior under high temperature the results are shown in Table 2, and thermal coefficient analysis the results are shown in Table 3.
Table 2 Examples 1 to 4 brake disc of high-speed train Heat-Treatment of Steel technique and mechanical behavior under high temperature
3 Examples 1 to 4 brake disc of high-speed train of table steel thermal coefficient at different temperatures
The crystallite dimension of the brake disc of high-speed train that each embodiment obtains steel is 20~25 μm, carbide average grain diameter
Between 0.020 μm~0.040 μm, tissue is tempered sorbite, is produced through 20 DEG C~700 DEG C cold cyclings, 1000 flawlesses
It is raw.
From in table 2,3 as can be seen that obtained brake disc of high-speed train steel the leading in 20 DEG C~700 DEG C of each embodiment
Hot coefficient is 35~40W/ (mK), 500 DEG C of tensile strength >=1000MPa, 600 DEG C of tensile strength >=900MPa.
Comparative example 1~4
A kind of brake disc of high-speed train steel, chemical component and weight percent are as shown in table 4:
The chemical component and weight percent of 4 comparative example of table, 1~4 high speed train brake disk steel
The preparation method of the brake disc of high-speed train steel includes following technique: electric arc furnaces or converter smelting → LF furnace essence
Refining → RH or VD vacuum outgas → continuous casting → slab heating stove heating → brake disc with round rolling → brake disc blank forging →
Normalizing+Tempering and Quenching → machining → flaw detection.It is heated to be rolled intoRound steel, then heated it is forged into brake disc
Blank carries out mechanical behavior under high temperature after table 5 is heat-treated, is finish-machined to drawing by high temperature and thermal coefficient sample with a thickness of 65mm
It is analyzed with thermal coefficient, the analysis of mechanical behavior under high temperature the results are shown in Table 5, and thermal coefficient analysis the results are shown in Table 6.
5 comparative example of table 1~4 brake disc of high-speed train Heat-Treatment of Steel technique and mechanical behavior under high temperature
6 comparative example of table, 1~4 brake disc of high-speed train steel thermal coefficient at different temperatures
The crystallite dimension of the brake disc of high-speed train that each comparative example obtains steel is 15 μm, and carbide average grain diameter exists
Between 0.060 μm~0.080 μm, tissue is tempered sorbite, has crackle production cold cycling 1000 times through 20 DEG C~700 DEG C
It is raw.As it can be seen that if by the parameter setting in the chemical component or heat treatment process of brake disc of high-speed train steel in the present invention
Except scope of disclosure, the high-temperature behavior of obtained brake disc of high-speed train steel difference more of the present invention.
A kind of above-mentioned detailed description brake disc of high-speed train carried out with steel referring to embodiment, be it is illustrative rather than
Limited, several embodiments, therefore the change in the case where not departing from present general inventive concept can be enumerated according to limited range
Change and modify, should belong within protection scope of the present invention.
Claims (9)
1. a kind of brake disc of high-speed train steel, which is characterized in that including following chemical component and mass percent: C:0.26
~0.28%, Si:0.30~0.35%, Mn:0.32~0.35%, Cr:1.08~1.38%, W:0.40~0.50%, Mo:0.58~
0.73%, Al :≤0.025%, V:0.75~0.90%, Co:0.30~0.35%, Ni :≤0.18%, Cu :≤0.20%, N :≤
0.0050%, P≤0.009%, S≤0.002%, surplus are Fe and inevitable impurity；And meet 0.9C≤0.03W+
0.063Mo+0.06Cr+0.2V≤1.1C。
2. brake disc of high-speed train steel according to claim 1, which is characterized in that the brake disc of high-speed train steel
Crystallite dimension be 20 ~ 25 μm, carbide average grain diameter is organized between 0.020 μm ~ 0.040 μm as tempered sorbite, 20 DEG C
~ 700 DEG C of thermal coefficients are 35 ~ 40 W/ (mK), 500 DEG C of tensile strength >=1000MPa, 600 DEG C of tensile strength >=900MPa.
3. brake disc of high-speed train steel according to claim 1, which is characterized in that the brake disc of high-speed train steel
Preparation method include following technique: electric arc furnaces or converter smelting → LF furnace refining → RH or VD vacuum outgas → continuous casting → slab
Heat the round rolling → brake disc blank forging → normalizing+Tempering and Quenching → machining → flaw detection of stove heating → brake disc.
4. brake disc of high-speed train steel according to claim 3, which is characterized in that the normalizing+Tempering and Quenching work
Skill includes normalizing process, quenching technical and tempering process.
5. brake disc of high-speed train steel according to claim 4, which is characterized in that in the normalizing process, normalizing temperature
1000 ~ 1100 DEG C, soaking time 5 ~ 8 hours of degree.
6. brake disc of high-speed train steel according to claim 4 or 5, which is characterized in that in the quenching technical, quenching
Temperature is 980 ~ 1020 DEG C, and soaking time 4 ~ 6 hours, hardening media was the PAG quenching liquid of 5% ~ 12% mass concentration.
7. brake disc of high-speed train steel according to claim 4 or 5, which is characterized in that in the tempering process, tempering
Temperature is 600 ~ 650 DEG C, and tempering insulation time is 5 ~ 8 hours.
8. brake disc of high-speed train steel according to claim 4, which is characterized in that further include air-cooled after normalizing process.
9. brake disc of high-speed train steel according to claim 4, which is characterized in that further include water cooling after tempering process.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201711033158.9A CN107746915B (en) | 2017-10-30 | 2017-10-30 | A kind of brake disc of high-speed train steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201711033158.9A CN107746915B (en) | 2017-10-30 | 2017-10-30 | A kind of brake disc of high-speed train steel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN107746915A CN107746915A (en) | 2018-03-02 |
| CN107746915B true CN107746915B (en) | 2019-02-22 |
Family
ID=61253330
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201711033158.9A Active CN107746915B (en) | 2017-10-30 | 2017-10-30 | A kind of brake disc of high-speed train steel |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN107746915B (en) |
Families Citing this family (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110899329B (en) * | 2019-10-25 | 2021-08-20 | 邯郸钢铁集团有限责任公司 | Method for producing brake pad back steel based on CSP continuous casting and rolling production line |
| CN110805633B (en) * | 2019-10-29 | 2021-01-22 | 中车长春轨道客车股份有限公司 | Friction-resistant brake block of high-speed train and preparation method thereof |
| CN110792707B (en) * | 2019-10-29 | 2021-01-22 | 中车长春轨道客车股份有限公司 | Friction-resistant brake block for high-speed train |
| CN110923580B (en) * | 2019-11-19 | 2021-07-02 | 马鞍山钢铁股份有限公司 | Heat-resistant 12.9-grade steel for fasteners for rail transit and heat treatment process thereof |
| 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 |
| CN113652600A (en) * | 2021-07-02 | 2021-11-16 | 南京钢铁有限公司 | Steel for brake disc of high-speed rail and heat treatment method thereof |
| CN113802068B (en) * | 2021-09-18 | 2022-03-04 | 建龙北满特殊钢有限责任公司 | Alloy structural steel containing tungsten and production method thereof |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 |
-
2017
- 2017-10-30 CN CN201711033158.9A patent/CN107746915B/en active Active
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 |
Also Published As
| Publication number | Publication date |
|---|---|
| CN107746915A (en) | 2018-03-02 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN107746915B (en) | A kind of brake disc of high-speed train steel | |
| CN106967929B (en) | A kind of forging of EMU brake disc mild steel and its heat treatment method | |
| WO2015197007A1 (en) | Carburized alloy steel, method for preparing same, and use thereof | |
| CN107760838B (en) | A kind of brake disc of high-speed train Heat-Treatment of Steel method | |
| CN105886904B (en) | A kind of steel of axle of motor train unit containing vanadium, its production method and Technology for Heating Processing | |
| CN108220807B (en) | Low-density high-aluminum ultrahigh-carbon bearing steel and preparation method thereof | |
| CN104004968B (en) | Wheel steel and wheel heat treatment method | |
| CN107267864B (en) | A kind of high-strength spring steel | |
| CN111748739B (en) | Heat-resistant spring steel with tensile strength of more than 2100MPa and production method thereof | |
| JP2004315890A (en) | Steel having excellent rolling fatigue life, and its production method | |
| CN104726819A (en) | Heat treatment carburization process of carburizing steel | |
| CN108998725A (en) | Track link rail 35MnBM steel and preparation method thereof | |
| CN106435367B (en) | A kind of bainite rail and preparation method thereof | |
| CN106756509B (en) | A kind of high-temperature alloy structural steel and its Technology for Heating Processing | |
| CN103352170A (en) | Alloy forged steel and production method and application thereof | |
| CN111850393B (en) | Bainite die steel and preparation method thereof | |
| CN107760992A (en) | A kind of tungstenic brake disc of high-speed train steel | |
| CN110819901B (en) | High-strength brake disc bolt steel and heat treatment process thereof | |
| CN107760991B (en) | A kind of steel of brake disc of high-speed train containing cobalt | |
| CN110923580B (en) | Heat-resistant 12.9-grade steel for fasteners for rail transit and heat treatment process thereof | |
| CN107641696A (en) | A kind of Heat-Treatment of Steel method of brake disc of high-speed train containing cobalt | |
| CN107760833B (en) | A kind of tungstenic brake disc of high-speed train Heat-Treatment of Steel method | |
| JP4212132B2 (en) | Ferritic heat resistant steel having martensitic structure and method for producing the same | |
| CN104480400B (en) | A kind of C-N-B composite hardening high wear-resisting cold process mould steel | |
| CN115747645B (en) | Steel for high-strength high-contact fatigue high-power wind power yaw bearing ring, bearing ring and production process |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |