CN107460362A - A kind of High Speed Railway Trains brake pad material and preparation method thereof - Google Patents
A kind of High Speed Railway Trains brake pad material and preparation method thereof Download PDFInfo
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- CN107460362A CN107460362A CN201710685182.4A CN201710685182A CN107460362A CN 107460362 A CN107460362 A CN 107460362A CN 201710685182 A CN201710685182 A CN 201710685182A CN 107460362 A CN107460362 A CN 107460362A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C9/00—Alloys based on copper
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/10—Metallic powder containing lubricating or binding agents; Metallic powder containing organic material
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/10—Metallic powder containing lubricating or binding agents; Metallic powder containing organic material
- B22F1/103—Metallic powder containing lubricating or binding agents; Metallic powder containing organic material containing an organic binding agent comprising a mixture of, or obtained by reaction of, two or more components other than a solvent or a lubricating agent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/05—Mixtures of metal powder with non-metallic powder
- C22C1/058—Mixtures of metal powder with non-metallic powder by reaction sintering (i.e. gasless reaction starting from a mixture of solid metal compounds)
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
- C22C30/02—Alloys containing less than 50% by weight of each constituent containing copper
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0005—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with at least one oxide and at least one of carbides, nitrides, borides or silicides as the main non-metallic constituents
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0084—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ carbon or graphite as the main non-metallic constituent
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
- F16D69/00—Friction linings; Attachment thereof; Selection of coacting friction substances or surfaces
- F16D69/02—Compositions of linings; Methods of manufacturing
- F16D69/027—Compositions based on metals or inorganic oxides
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
Abstract
The invention discloses a kind of High Speed Railway Trains brake pad material and preparation method thereof, belong to powder metallurgy friction material technical field.The brake pad material is by will put into batch mixer after the dry screening of raw material dried bean noodles, spray into binding agent, be placed in steel die and suppress after batch mixing, then sinter under reducing atmosphere, then made of being heat-treated under reducing atmosphere；Wherein, the raw material powder is copper powder, iron powder, Ti2AlC powder, chromium powder, nickel powder, manganese powder, silica, graphite, boron nitride and molybdenum disulfide.Present invention also offers the preparation method of the brake pad material.The present invention is to pass through Ti2The in_situ TiC that AlC is obtained is main friction component, prepares the material of in-situ nano TiC lamella skeletons, and then using copper as matrix, adds the content of the lubricant component such as other a small amount of metals, regulation graphite, finally obtain the new material that braking effect is excellent, wear rate is low.It is suitable as High Speed Railway Trains brake pad material.
Description
Technical field
The present invention relates to a kind of High Speed Railway Trains brake pad material and preparation method thereof, belong to powder metallurgy friction
Field of material technology.
Background technology
The foundation brake mode of train is a lot, such as friction catch, resistive braking, track eddy-current brake, wherein with friction
Brake application is wider.Friction catch can be divided into two kinds of tread brake and disc braking again, and the former braking member is brake shoe, and the latter is then
For brake puck/brake lining friction pair.With the rapid development of the national economy, the high speed of railway transportation turns into inexorable trend,
Particularly speed per hour is in 300km and the high-speed railway of the above positive acquisition tremendous development, and the continuous improvement of train speed is made to it
Dynamic performance it is also proposed more stringent requirement.The brake efficiency of tread brake can not meet needs, and brake shoe is at a high speed
It is difficult to play a role on train, brake pad material just turns into the ring of core one of bullet train friction catch.
Brake puck/brake lining friction catch mode requires that brake lining material friction coefficient is high, and abrasion resistance properties are excellent.It experienced
Cast iron, Composition brake shoes, iron-based and copper-based sintering brake lining stage, and to other advanced composite material (ACM)s and C/C composites brake lining/
The shortcomings that watt stage development, wherein cast iron materials most serious is that have compatibility, serious wear with mating material；Organic synthesis material
Material long-term use can grind antithesis to obtain unusual light, reduce coefficient of friction, while be difficult in adapt to high temperature and high pressure condition；Carbon carbon is compound
Material cost is too high, is usually used in aircraft braking；Only powdered metallurgical material can meet performance requirement at present, have warp again
Ji applicability.
Powdered metallurgical material is also known as sintered metal materials, is using metal and alloy as matrix, adds other constituent elements, use powder
Composite made of metallurgical technology, it is a kind of pseudo-alloy containing metal and nonmetal multicomponent, includes matrix constituent element, friction group
Member and lubricant component.Since nineteen twenty-nine occurs, by researching and developing for many years, powdered metallurgical material has become a kind of important
Engineering material.
Influence of the selection of powdered metallurgical material friction component to material overall performance is most important, because friction component rises
To the effect for improving coefficient of friction, as main hard phase of the material in friction process, its brake efficiency to material and rub
It is huge to wipe stationarity influence.Traditional friction component has oxide such as silica etc.；Carbide ceramics such as titanium carbide etc.；Hard
Metal such as tungsten, molybdenum etc..But these conventional friction constituent elements there is it is different the problem of, as oxide, carbide ceramics have hardness
Too high, the problem of secondary both sides cause wear rate high is matched somebody with somebody in damage；There is coefficient of friction deficiency in hard metal material, brake efficiency difference
Problem.New constituent element such as Ti3AlC2Also it is added in Copper substrate Deng ternary layered ceramic and is used as friction material, but itself is made
It is relatively low for friction component hardness, it is difficult to independently increase to rub mutually to play as hard during bullet train friction catch to significantly improve
The effect of coefficient of friction, it is used as the particle strengthening material of pantograph etc. because it possesses certain self-lubricating property on the contrary.
Copper is the metal material that electric conductivity is only second to silver, is widely used in electric friction field, but intensity is relatively low wears no resistance；
It is the preferable enhancing phase of metal and titanium carbide possesses high intensity, hardness and high heat conduction, conductive characteristic.Therefore the two advantage is combined
Titanium carbide enhancing copper-based material possess wide application prospect in electric friction field.With directly adding titanium carbide phase in Copper substrate
Than, in-situ carburization titanium enhancing Cu-base composites because wetability is good, interface binding power is strong, its various aspects of performance exceedes direct
Its composite with copper prepared by titanium carbide is added, thus in-situ carburization titanium strengthens the researching value of Cu-base composites and answered
It is all even more important and wide with prospect.
Common in-situ carburization titanium addition manner mainly by reaction method in chemical synthesis, common Ti sources have Ti powder,
TiO2There are carbon black, CNT etc. Deng, C sources, this addition manner mainly passes through Ti sources under raw material addition Copper substrate high temperature
It is made with the reaction of C sources.But there is also the problems such as such as raw material reaction of many problems is incomplete, generation TiC shape sizes are unmanageable.
Research in recent years finds that ternary layered compound can decompose under copper high temperature environment, has been related to utilize
Ti3AlC2、Ti2AlC etc. decomposition prepares the report of in_situ TiC enhancing copper-based material, is prepared more by simple heat pressing process,
Catabolite and tissue still exist with spherical particle more, are not related to and tissue and frictional behaviour are discussed in detail, more not in height
The correlated performance report of fast friction field.
The content of the invention
Hard ceramic particles etc. are added in order to increase coefficient of friction to solve traditional brake lining material, but Presence of an interface combines by force
The problems such as insufficient is spent, then hard particles come off interface bond strength deficiency, cause wear rate to raise, while because hard particles are gradual
Come off the problems such as causing frictional decrease and occur.The invention provides a kind of High Speed Railway Trains brake pad material and its
Preparation method, be related to it is a kind of with particular tissues and frictional behaviour it is excellent in-situ carburization titanium enhancing copper (iron) based composites and
Its preparation method, the friction catch for High Speed Railway Trains.The technical scheme of use is as follows：
It is an object of the invention to provide a kind of High Speed Railway Trains brake pad material, the material is by by raw material
Batch mixer is put into after the dry screening of dried bean noodles, binding agent is sprayed into, is placed in steel die and suppresses after batch mixing, then burn under reducing atmosphere
Knot, then made of being heat-treated under reducing atmosphere；Wherein, the raw material powder is copper powder, iron powder, Ti2AlC powder, chromium powder, nickel
Powder, manganese powder, silica, graphite, boron nitride and molybdenum disulfide.
Further, the Ti2The stoichiometric proportion of AlC powder is 2:1:0.7.
Further, copper powder 45%~73%, iron powder 2%~18%, Ti2AlC powder 1%~12%, chromium powder 2%~
10%th, nickel powder 0.2%~3%, manganese powder 0.2%~3%, silica 0.2%-2%, graphite 6%~19%, boron nitride
0.2%~2%, molybdenum disulfide 0.2%~2%.
Further, copper powder 57%~62%, iron powder 2%~12%, Ti2AlC powder 7%~12%, chromium powder 5%~
8.5%th, nickel powder 0.5%~3%, manganese powder 0.5%~3%, silica 1 %-2%, graphite 6%~12%, boron nitride 1%~
2%th, molybdenum disulfide 1.5%~2%.
Further, the weight/mass percentage composition of each composition is in the raw material powder：Copper powder 57%, iron powder 12%,
Ti2AlC powder 7%, chromium powder 5%, nickel powder 0.5%, manganese powder 0.5%, silica 2%, graphite 12%, boron nitride 2%, curing
Molybdenum 2%.
Present invention also offers a kind of preparation method of above-mentioned brake pad material, it is characterised in that is according to following step
Suddenly prepared：
1) batch mixing：By raw material powder by drying, sieve, weigh after put into batch mixer, spray into binding agent, batch mixing 2h-5h；
2) prefabricated pressed compact：It will be put into steel grinding tool and suppress by the mixed raw material of step 1), load 300MPa~
500MPa；
3) sinter：Under reducing atmosphere, 850 DEG C of sintering temperature is warming up to 10 DEG C/min~20 DEG C/min heating rate
~980 DEG C, while be forced into 30MPa~50MPa, it is incubated 1h-2h, keeps pressure 0.5h and then be depressurized to while insulation
1MPa~5MPa, insulation terminate rear furnace cooling, the unloading pressure when furnace temperature is less than 600 DEG C；
4) it is heat-treated：Under reducing atmosphere, 600 DEG C are warming up to 20 DEG C/min~30 DEG C/min heating rate, insulation
0.5h-1h, it is heat-treated 5 times~10 times according to above-mentioned heat treatment method.
Further, the binding agent described in step 1) is by the kerosene of 95% (quality) and the Acidic phosphates of 5% (quality)
Ester forms.
Further, the binding agent described in step 1) adds according to the 1%-5% (quality) of raw material powder gross mass.
Further, the load described in step 2) is 400MPa.
Further, step 3) is under reducing atmosphere, sintering temperature 980 to be warming up to 10 DEG C/min heating rate
DEG C, while 30MPa is forced into, keeping temperature 2h, keeps pressure 0.5h and then be depressurized to 1MPa while insulation, insulation terminates
Rear furnace cooling, the unloading pressure when furnace temperature is less than 600 DEG C.
Further, step 4) is under reducing atmosphere, to be warming up to 600 DEG C with 20 DEG C/min heating rate, insulation
0.5h, it is heat-treated 5 times according to above-mentioned heat treatment method.
The principle of the invention：
Traditional Ti2The stoichiometric proportion of AlC powder is 2:1:1, and the Ti used in brake lining material is prepared in the present invention2AlC powder
System is synthesized by self- propagating technique, and by adjust raw material titanium valve, aluminium powder, carbon black molar ratio be 3:1.4:0.8, warp
It is Ti to cross self- propagating technique and obtain chemical coefficient ratio：Al：C=2:1:The vacant Ti of 0.7 C stoichiometric proportions2AlC powders,
The present inventor has found in experimentation：For in_situ TiC in growth course is formed, its C stoichiometric proportion is lower,
TiC more tends to be formed sheet, when C stoichiometric proportion is higher or reaches complete stoichiometric proportion 1, its form closer to
The main reason for spheroid here it is situ TiC of the present invention is sheet, in addition brake lining sintering process used in the present invention and
Technology for Heating Processing also promotes the formation of this sheet TiC tissue, the larger sintering pressure of holding stage and is sintering
Bi Fanfu heat treatment process has been obviously promoted Ti2Conversions of the AlC to sheet TiC, and stabilize this sheet tissue.
The in_situ TiC synthetic technology or utilization and Ti that other techniques use2A kind of compound (such as Ti similar AlC3AlC2)
The in_situ TiC prepared is decomposed, the vacant degree of its C atom is relatively low, while lacks technique to stablize this tissue, causes other special
The generation of rare this tissue in profit, or even if having allied organization also without good technique come the property stablizing to it and obtained
Energy.
This intimate nano-scale of in_situ TiC lamella that the present invention is formed, the nano reinforcement effect of diffusing particle is formed, together
When Ti2Al in AlC is dissolved into Cu matrixes, formed solution strengthening, dual reinforcing effect simultaneously improve material intensity and
Plasticity and toughness, it is different from granular carbonization titanium that nanometer sheet stratiform is organized in its Breakage Mechanism in process of friction and wear, will not integrally take off
Fall, the 3rd body abrasive particle of bulky grain will not be produced, reduce wear rate, degree reduces simultaneously as it comes off, and can maintain higher
Coefficient of friction.
The present invention is to pass through Ti2The in_situ TiC that AlC is obtained is main friction component, there is provided a kind of by specifically adding
Pressure sintering, extruding and Technology for Heating Processing, obtain the method (Fig. 1) of in-situ nano TiC lamella skeletons.And then using copper as matrix, add
Add the content of the lubricant component such as other a small amount of metals, regulation graphite, finally obtain the new height that braking effect is excellent, wear rate is low
Fast railway brake brake lining material (Fig. 2).
With existing ternary layered ceramic (Ti3AlC2, Ti3SiC2Deng) Reinforced Cu sill compares, the present invention is to utilize three
First ceramics prepare in_situ TiC Reinforced Cu sill for raw material.With existing in-situ carbon compound enhancing copper-based material compared to (comprising with
Ternary ceramics Ti3AlC2、Ti2AlC etc. adds for raw material), by in-situ carburization titanium prepared by this patent technique in decomposition region point
(darker slice show TiC lamellas in Fig. 1, compared with light areas for cloth presentation nano-sheet distribution rather than common spherical distribution
For Cu matrixes), this nanoscale twins are in original Ti2AlC decomposition region is largely distributed and forms a nanometer skeleton, and by model
The interior adjustment to the technique is enclosed, this nanometer sheet can be adjusted especially by the control of heat treatment heating and cooling number and temperature
The lamella size and spacing and then performance of control of layer tissue.Performance of this nanometer skeleton in friction process also with it is traditional big
The hard particles of block aggregation also vary considerably (Fig. 3), under high temperature and high speed friction condition, titanium carbide lamella only understand breaking deformation and
The non-entirety as tradition enhancing mutually comes off and causes serious abrasive wear, and this nanometer skeleton can effectively reduce abrasion
Rate, the scuffing with secondary steel disk is particularly avoided, multiple 1:Under the test of 10 bench simulation 350km/h braking conditions, brake lining is average
Wear rate only has 0.08cm3/ MJ, with secondary steel disk surface without obvious cut, only national standard 0.35cm3The 1/3 of/MJ is less than property
Can be excellent.
The main advantage of the present invention is：1st, a kind of group of new in-situ carbon compound enhancing metal_based material is obtained
Knit, by special sintering and Technology for Heating Processing, utilize Ti2AlC decomposition obtains big face in its primary granule distributed areas
The TiC lamellas skeleton (Fig. 1) of product in-situ nano yardstick.2nd, the form of this tissue and performance are controllable, by change sintering pressure,
The parameter such as the temperature of heat treatment and number can control the lamellar spacing of in_situ TiC and spacing and then control TiC lamella skeletons
Hardness, so as to influence other friction and wear behaviors such as coefficient of friction and friction stability.3rd, wear rate is low, with in_situ TiC lamella
Enhancing region is that increasing rubs phase, can only be deformed in friction process with it is microcosmic it is broken will not integrally deviate from (Fig. 3), cleverly solve
Tradition strengthens the problem of phase excessive high hardness, deformability are poor and basal body binding force is weak, is provided simultaneously with high thermal conductivity.4th, conduct
High-speed railway brake pad material properties are excellent, compression strength more than 110MPa, shear strength in more than 20MPa, rub
Coefficient is wiped more than 0.31 (1:10 high-speed railways brake simulating bench test result as shown in figure 4, braking initial velocity is
350km/h, calculate and understand by Y-axis 100=0.9 coefficient of friction, whole instantaneous coefficient of friction is more than 0.31), and control
Provide within variable range, relatively more steady, wear rate 0.08cm3/ MJ, is far more than 0.35cm3/ MJ national standard.
A kind of Ti used for high-speed railway is disclosed in patent CN 103302283A3ALC2Strengthen bronze base brake pad material and
Its preparation method, the enhancing of its brake lining material obtained is mutually graininess, the original position for not possessing the sheet that the present invention is obtained
TiC institutional frameworks, coefficient of friction is relatively low compared with the brake lining material of invention, and wear rate is higher, and interface cohesion is poor.
Beneficial effect of the present invention：
1st, the Ti used in the present invention2AlC powders system is synthesized by self- propagating technique, and by adjusting raw material titanium valve, aluminium
It is Ti that powder, the ratio of carbon black, which obtain chemical coefficient ratio,：Al：C=2:1:The vacant Ti of 0.7 C stoichiometric proportions2AlC powders,
The powder forms a kind of laminar structured, this laminar structured this sheet tissue during in_situ TiC is generated
Simple in-situ carburization titanium (graininess is spherical) is different from, its friction and wear behavior is more excellent, in process of friction and wear
Its Breakage Mechanism is different from granular carbonization titanium, will not integrally come off, and will not produce the 3rd body abrasive particle of bulky grain, reduces abrasion
Rate, simultaneously as it comes off, degree reduces, and can maintain higher coefficient of friction.
2nd, brake lining sintering process and Technology for Heating Processing used in the present invention also promotes this sheet TiC tissues in addition
Formation, the larger sintering pressure of holding stage and be obviously promoted Ti in the heat treatment process that finishes repeatedly of sintering2AlC to
Sheet TiC conversion, and stabilize this sheet tissue.
3rd, this intimate nano-scale of in_situ TiC lamella that the present invention is formed, nano reinforcement, while Ti are formed2In AlC
Al is dissolved into Cu matrixes, forms solution strengthening, and dual reinforcing effect improves the intensity and plasticity and toughness of material, nanometer sheet simultaneously
Lamellar tissue's its Breakage Mechanism in process of friction and wear is different from granular carbonization titanium, will not integrally come off, and will not produce big
3rd body abrasive particle of particle, wear rate is reduced, degree reduces simultaneously as it comes off, and can maintain higher coefficient of friction.
4th, the binding agent that uses of the present invention, solves the problems, such as batch mixing difficulty caused by copper graphite density unevenness, while
Volatilized under high temperature almost noresidue.The effect of wherein kerosene is binding agent, and the effect of dialkyl phosphate is that further improve is glued
Degree, mixed effect is more preferable, while binding agent volatilization is more thorough in heating process.
5th, the present invention created using ternary ceramic material prepare in_situ TiC enhancing Copper substrate material one kind prepare work
Skill, its similar with other in-situ method generation TiC difference be, can by the use of the special process and raw material of the present invention
Tissue topography as shown in Figure 1 is obtained, this pattern has double dominant to strengthening effect and frictional behaviour lifting.What the present invention obtained
Material is as the advantage of brake lining material：1st, brake lining material matrix intensity deficiency, the brake lining of other patents are solved the problems, such as
Material is also intended to strengthen matrix by various ways and means, but enhancing be present and mutually combined with matrix loosely, and it is weaker to strengthen effect
Problem, this in_situ TiC of the invention natively possess the high advantage of interface bond strength because being generated in material,
Bring the lifting for strengthening effect；2nd, this sheet tissue such as Fig. 1, also brings the lifting of friction and wear behavior, this
Layer tissue can produce hard particles and increase the effect rubbed, and come off, carrying simultaneously because its failure mode is different from conventional rigid particle
While rising coefficient of friction, the rise of wear rate is avoided, while plays the role of stable coefficient of friction, bench test results are as schemed
4 also indicate that, develop the coefficient of friction requirement that brake lining material friction coefficient has met 250-350km/h speed per hour braking conditions,
The very little of coefficient of friction fluctuation simultaneously, overall wear rate 0.08cm3/ MJ, also fully meet requirement.Other brake lining materials are typically deposited
In standard friction coefficient, but the situation that coefficient of friction fluctuation is big or wear rate is higher, the brake lining material that the present invention develops, well
The problem of balancing coefficient of friction, wear rate, stable friction factor, realize the comprehensive lifting of friction and wear behavior.3rd, it is same
When this tissue can be controlled by technique, thus its performance is also moderately to adjust, and high ferro vehicle is numerous, this
Characteristic by process tunability energy is also important.
Brief description of the drawings
Fig. 1 is in_situ TiC lamella skeleton；
(A, transmission electron microscope；B, ESEM).
Fig. 2 is brake pad material finished figure.
Fig. 3 is in-situ produced SiC particulate friction operation principle.
Fig. 4 is brake lining material engine bench test friction coefficient curve.
Fig. 5 is the ESEM of the in_situ TiC Reinforced Cu matrix region of brake lining material prepared by control experiment in embodiment 1
Figure (enhancing is mutually graininess rather than lamella).
Embodiment
With reference to specific embodiment, the present invention will be further described, but the present invention should not be limited by the examples.
Embodiment 1：
First, Ti2The preparation method of AlC powder
By titanium valve, aluminium powder and carbon black according to mol ratio 3:1.4:0.8 is mixed, and is then protected without pressurization, inert gas
It is 2 that shield, which is lighted by self- propagating technique synthesis stoichiometric proportion,:1:0.7 Ti2AlC powder.
2nd, the preparation method of binding agent
Binding agent is made up of the kerosene of 95% (quality) and the dialkyl phosphate of 5% (quality).Binding agent is according to raw material
1%-5% (quality) additions of powder gross mass.
Found through experiment：It is best according to 5% (quality) additive effect of raw material powder gross mass.Prepared according to aforementioned proportion
Binding agent, solve the problems, such as batch mixing difficulty caused by copper graphite density unevenness, while almost noresidue of volatilizing at high temperature.Its
The effect of middle kerosene is binding agent, and the effect of dialkyl phosphate is further raising viscosity, and mixed effect is more preferable, heats simultaneously
During binding agent volatilization it is more thorough.
3rd, it is a kind of that there is laminar structured High Speed Railway Trains brake pad material preparation method (in-situ preparation
TiC)：
The brake pad material of the present embodiment be by putting into batch mixer after the dry screening of raw material dried bean noodles, spraying into binding agent,
It is placed in steel die and suppresses after batch mixing, then sinters under reducing atmosphere, then made of being heat-treated under reducing atmosphere；
Wherein, the raw material powder is copper powder, iron powder, Ti2AlC powder, chromium powder, nickel powder, manganese powder, silica, graphite, boron nitride and two sulphur
Change molybdenum.
The weight/mass percentage composition of each composition is in raw material powder：Copper powder 45%~73%, iron powder 2%~18%, Ti2AlC powder
1%~12%, chromium powder 2%~10%, nickel powder 0.2%~3%, manganese powder 0.2%~3%, silica 0.2%-2%, graphite
6%~19%, boron nitride 0.2%~2%, molybdenum disulfide 0.2%~2%.
Further preferred scope is：Copper powder 57%~62%, iron powder 2%~12%, Ti2AlC powder 7%~12%, chromium powder
5%~8.5%, nickel powder 0.5%~3%, manganese powder 0.5%~3%, silica 1 %-2%, graphite 6%~12%, boron nitride
1%~2%, molybdenum disulfide 1.5%~2%.
Brake pad material can follow the steps below preparation：
1) batch mixing：By raw material powder by drying, sieve, weigh after put into batch mixer, spray into binding agent, batch mixing 2h-5h；
2) prefabricated pressed compact：It will be put into steel grinding tool and suppress by the mixed raw material of step 1), load 300MPa~
500MPa；
3) sinter：Under reducing atmosphere, 850 DEG C of sintering temperature is warming up to 10 DEG C/min~20 DEG C/min heating rate
~980 DEG C, while be forced into 30MPa~50MPa, it is incubated 1h-2h, keeps pressure 0.5h and then be depressurized to while insulation
1MPa~5MPa, insulation terminate rear furnace cooling, the unloading pressure when furnace temperature is less than 600 DEG C；
4) it is heat-treated：Under reducing atmosphere, 600 DEG C are warming up to 20 DEG C/min~30 DEG C/min heating rate, insulation
0.5h-1h, it is heat-treated 5 times~10 times according to above-mentioned heat treatment method.
Embodiment 2
Pass through the effect of the following description of test present invention：
The present embodiment prepares brake lining material, specific formula such as table 1 according to following specific formula and preferred forms respectively
It is shown.
The preferred forms of the preparation method of brake lining material are in embodiment 1：
1) batch mixing：By raw material powder by drying, sieve, weigh after put into batch mixer, spray into binding agent, batch mixing 2h；
2) prefabricated pressed compact：It will be put into steel grinding tool and suppress by the mixed raw material of step 1), load 400MPa；
3) sinter：Under reducing atmosphere, 980 DEG C of sintering temperature is warming up to 10 DEG C/min heating rate, pressurizeed simultaneously
To 30MPa, keeping temperature 2h, keep pressure 0.5h and then be depressurized to 1MPa while insulation, insulation terminate after after it is cold with stove
But, the unloading pressure when furnace temperature is less than 600 DEG C；
4) it is heat-treated：Under reducing atmosphere, 600 DEG C are warming up to 20 DEG C/min heating rate, 0.5h are incubated, according to upper
Heat treatment method is stated to be heat-treated 5 times.
The composition of raw materials of table 1
Control experiment：Difference with experiment 2 is Ti2The preparation method of AlC powder is different, Ti2AlC powder uses conventional method
Prepare, specific method is as follows：By titanium valve, aluminium powder and carbon black according to mass ratio be 3:1.4:0.8 is mixed, then without pressurization
Self- propagating technique synthesis Ti is carried out under inert gas conditions2AlC powder.Other raw material components and content, and the system of brake lining material
Preparation Method is identical with experiment 1.
The brake pad material prepared according to experiment 1, experiment 2, experiment 3 and control experiment is subjected to performance and structure ratio
It is right, as a result as shown in table 2.
The experiment of table 21, experiment 2, the performance and structure alignment for testing 3 and control group
| Compression strength MPa | Coefficient of friction | Wear rate cm3/MJ | In_situ TiC structure | |
| Experiment 1 | 125 | 0.33 | 0.18 | Sheet |
| Experiment 2 | 130 | 0.34 | 0.10 | Sheet |
| Experiment 3 | 127 | 0.34 | 0.13 | Sheet |
| Experiment 4 | 110 | 0.32 | 0.16 | Sheet |
| Control experiment | 90 | 0.28 | 0.31 | Graininess |
Understand that experiment 2 be optimum embodiment by table 2, experiment 3 is taken second place, experiment 1 third, according to experiment 2 formula with
The brake pad material finished figure that preparation method obtains is as shown in Figure 2.Fig. 3 is in-situ produced SiC particulate friction operation schematic diagram, this hair
The brake pad material wear rate of bright acquisition is low, is that increasing rubs phase using in_situ TiC lamella enhancing region, can become in friction process
Shape and it is microcosmic it is broken will not integrally deviate from (Fig. 3), cleverly solve that tradition enhancing phase excessive high hardness, deformability be poor and base
The problem of body adhesion is weak, it is provided simultaneously with high thermal conductivity.
The brake lining material prepared by using the inventive method, in sheet, (Fig. 1 is in_situ TiC to the structure ultimately formed
Lamella skeleton drawing, wherein A are transmission electron microscope；B is ESEM), this kind of structure is show clearly in Figure 1B and is existed on a large scale, is schemed
1A, which understands, presents in_situ TiC lamella skeleton, and the thickness of lamella is less than 100nm in Figure 1A, and the spacing between lamella is less than
100nm, generate nanoscale twins and strengthen effect.And control experiment is the Ti prepared by conventional method2AlC powder, by using
The method of the present invention prepares brake lining material, and for the TiC forms ultimately formed closer to spheroid (as shown in Figure 5), enhancing is in mutually
It is granular, rather than be sheet, this kind of granular structure does not possess a series of good characteristics of sheet TiC possesseds, particle
For shape structure compared with sheet, interface cohesion is poor, causes the problems such as coefficient of friction is insufficient, and wear rate is too high, strengthens effect also not
Such as sheet TiC, mechanical property is poor, and performance is markedly less than the brake lining material that sheet TiC is organized in this patent on the whole.Its
Fail to be formed the raw material Ti that the main reason for laminar structured is to select2AlC stoichiometric proportions are close to 2:1:1, C atom
Vacant deficiency, while without sintering and Technology for Heating Processing described in this patent is used, so being generated without sheet TiC.
Material (experiment 1-3), pressure resistance excellent as high-speed railway brake pad material properties that the present invention obtains
Degree more than 110MPa, shear strength more than 20MPa, coefficient of friction more than 0.31 (1:The braking simulation of 10 high-speed railways
Bench test results as shown in figure 4, braking initial velocity be 350km/h, by Y-axis 100=0.9 coefficient of friction calculate knowable to,
Whole instantaneous coefficient of friction is more than 0.31), and control within regulation variable range, relatively more steady, wear rate is
0.08cm3/ MJ, is far more than 0.35cm3/ MJ national standard.
Embodiment 3
The present embodiment and the difference of experiment 2 in embodiment 2 are：The preparation method of brake pad material is different, and other are equal
Identical with experiment 1, specific preparation method is：
1) batch mixing：It using material by wet type mixing, will be weighed after material powder drying, screening, and material powder put into batch mixer,
Spray into binding agent, batch mixing 2h；
2) prefabricated pressed compact：It will be put into steel grinding tool and suppress by the mixed raw material of step 1), load 300MPa；
3) sinter：It is sintered under reducing atmosphere, 850 DEG C of sintering temperature is warming up to 10 DEG C/min heating rate,
It is forced into 30MPa simultaneously, is incubated 1h, keeps pressure 0.5h and then be depressurized to 1MPa while insulation, insulation is cold with stove after terminating
But, the unloading pressure when furnace temperature is less than 600 DEG C；
4) it is heat-treated：Under reducing atmosphere, 600 DEG C are warming up to 20 DEG C/min heating rate, 0.5h are incubated, according to upper
Heat treatment method is stated to be heat-treated 5 times.
Embodiment 4
The present embodiment and the difference of experiment 2 in embodiment 2 are：The preparation method of brake pad material is different, and other are equal
Identical with experiment 1, specific preparation method is：
1) batch mixing：It using material by wet type mixing, will be weighed after material powder drying, screening, and material powder put into batch mixer,
Spray into binding agent, batch mixing 5h；
2) prefabricated pressed compact：It will be put into steel grinding tool and suppress by the mixed raw material of step 1), load 500MPa；
3) sinter：It is sintered under reducing atmosphere, 980 DEG C of sintering temperature is warming up to 20 DEG C/min heating rate,
It is forced into 50MPa simultaneously, is incubated 2h, keeps pressure 0.5h and then be depressurized to 5MPa while insulation, insulation is cold with stove after terminating
But, the unloading pressure when furnace temperature is less than 600 DEG C；
4) it is heat-treated：Under reducing atmosphere, 600 DEG C are warming up to 30 DEG C/min heating rate, 1h are incubated, according to above-mentioned
Heat treatment method is heat-treated 10 times.
For the processing analysis of the brake lining material of embodiment 2, embodiment 3 and embodiment 4, it is found through experiments that：Step
It is rapid 1) in mixing time using 2h be optimal, can now be well mixed, overlong time can cause graphite powder to be fragmented into granularity
Smaller particle.Prefabricated compacting pressure is using 400MPa to be optimal in step 2), and now compact strength is higher, sinters back brake piece hole
Rate is moderate, and brake lining friction and wear behavior is optimal.Step 3) and 4) using each technological parameter in embodiment 2 as it is optimal (i.e.：Step 3)
It is under reducing atmosphere, 980 DEG C of sintering temperature to be warming up to 10 DEG C/min heating rate, while is forced into 30MPa, keeps temperature
Spend 2h, pressure 0.5h kept while insulation and then is depressurized to 1MPa, insulation terminate after after furnace cooling, when furnace temperature is less than 600
DEG C when unloading pressure；Step 4) is under reducing atmosphere, to be warming up to 600 DEG C with 20 DEG C/min heating rate, be incubated 0.5h, press
It is heat-treated 5 times according to above-mentioned heat treatment method), the nanoscale twins tissue formed under the collective effect of two processing steps most adapts to
In the condition of work of fretting wear, coefficient of friction is high, and wear rate is low, and good mechanical performance.Therefore, the technique in embodiment 2
It is best for optimal embodiment, the product properties of acquisition.
Although the present invention is disclosed as above with preferred embodiment, it is not limited to the present invention, any to be familiar with this
The people of technology, without departing from the spirit and scope of the present invention, various changes and modification, therefore the protection of the present invention can be done
What scope should be defined by claims is defined.
Claims (10)
1. a kind of High Speed Railway Trains brake pad material, it is characterised in that the brake pad material is by by raw material
Batch mixer is put into after the dry screening of dried bean noodles, binding agent is sprayed into, is placed in steel die and suppresses after batch mixing, then burn under reducing atmosphere
Knot, then made of being heat-treated under reducing atmosphere；Wherein, the raw material powder is copper powder, iron powder, Ti2AlC powder, chromium powder, nickel
Powder, manganese powder, silica, graphite, boron nitride and molybdenum disulfide.
2. brake pad material according to claim 1, it is characterised in that the Ti2The stoichiometric proportion of AlC powder is 2:
1:0.7。
3. brake pad material according to claim 1, it is characterised in that the quality percentage of each composition in the raw material powder
Content is：Copper powder 45%~73%, iron powder 2%~18%, Ti2AlC powder 1%~12%, chromium powder 2%~10%, nickel powder 0.2%
~3%, manganese powder 0.2%~3%, silica 0.2%-2%, graphite 6%~19%, boron nitride 0.2%~2%, curing
Molybdenum 0.2%~2%.
4. brake pad material according to claim 1, it is characterised in that the quality percentage of each composition in the raw material powder
Content is：Copper powder 57%, iron powder 12%, Ti2AlC powder 7%, chromium powder 5%, nickel powder 0.5%, manganese powder 0.5%, silica 2%,
Graphite 12%, boron nitride 2%, molybdenum disulfide 2%.
5. the preparation method of the brake pad material described in a kind of claim 1, it is characterised in that be to follow the steps below
Prepare：
1) batch mixing：By raw material powder by drying, sieve, weigh after put into batch mixer, spray into binding agent, batch mixing 2h-5h；
2) prefabricated pressed compact：It will be put into steel grinding tool and suppress by the mixed raw material of step 1), load 300MPa~500MPa；
3) sinter：Under reducing atmosphere, with 10 DEG C/min~20 DEG C/min heating rate be warming up to 850 DEG C of sintering temperature~
980 DEG C, while be forced into 30MPa~50MPa, it is incubated 1h-2h, keeps pressure 0.5h and then be depressurized to 1MPa while insulation
~5MPa, insulation terminate rear furnace cooling, the unloading pressure when furnace temperature is less than 600 DEG C；
4) it is heat-treated：Under reducing atmosphere, 600 DEG C are warming up to 20 DEG C/min~30 DEG C/min heating rate, are incubated 0.5h-
1h, it is heat-treated 5 times~10 times according to above-mentioned heat treatment method.
6. according to the method for claim 5, it is characterised in that binding agent described in step 1) by 95% (quality) kerosene
Formed with the dialkyl phosphate of 5% (quality).
7. according to the method for claim 5, it is characterised in that the binding agent described in step 1) is according to raw material powder gross mass
1%-5% (quality) is added.
8. according to the method for claim 5, it is characterised in that the load described in step 2) is 400MPa.
9. according to the method for claim 5, it is characterised in that step 3) is under reducing atmosphere, with 10 DEG C/min liter
Warm speed is warming up to 980 DEG C of sintering temperature, while is forced into 30MPa, keeping temperature 2h, keep while insulation pressure 0.5h,
Then 1MPa, insulation rear furnace cooling after terminating, the unloading pressure when furnace temperature is less than 600 DEG C are depressurized to.
10. according to the method for claim 5, it is characterised in that step 4) is under reducing atmosphere, with 20 DEG C/min liter
Warm speed is warming up to 600 DEG C, is incubated 0.5h, is heat-treated 5 times according to above-mentioned heat treatment method.
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| CN107630955A (en) * | 2017-08-14 | 2018-01-26 | 天津冶金职业技术学院 | A kind of powder metallurgy wear brake pad and preparation method thereof |
| CN109468493A (en) * | 2018-12-29 | 2019-03-15 | 大连大学 | A kind of preparation process of powder metallurgy Ni-Al base high temperature friction material |
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| CN109468493A (en) * | 2018-12-29 | 2019-03-15 | 大连大学 | A kind of preparation process of powder metallurgy Ni-Al base high temperature friction material |
| ES2774623A1 (en) * | 2019-08-30 | 2020-07-21 | Cofren Srl | DISC BRAKE SHOE FOR MEDIUM/LOW SPEED RAIL VEHICLES (Machine-translation by Google Translate, not legally binding) |
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| CN113234954A (en) * | 2021-04-30 | 2021-08-10 | 中铁隆昌铁路器材有限公司 | Copper-based powder metallurgy friction material and preparation method thereof |
| CN113512658A (en) * | 2021-06-17 | 2021-10-19 | 西安交通大学 | An inhibitor of Ti3AlC2Ni-doped Ti for decomposition3AlC2Cu composite material and preparation method thereof |
| CN113667852A (en) * | 2021-09-03 | 2021-11-19 | 合肥工业大学 | Powder metallurgy preparation method of high-thermal-conductivity Cu-Invar bimetal-based composite material |
| CN113667852B (en) * | 2021-09-03 | 2022-05-31 | 合肥工业大学 | Powder metallurgy preparation method of high-thermal-conductivity Cu-Invar bimetal-based composite material |
| CN114110062A (en) * | 2021-11-30 | 2022-03-01 | 湖南屹林材料技术有限公司 | Magnetic suspension train braking material and preparation technology thereof |
| CN114110062B (en) * | 2021-11-30 | 2024-04-09 | 湖南屹林材料技术有限公司 | Magnetic suspension train braking material and preparation technology thereof |
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| CN117144183A (en) * | 2023-09-13 | 2023-12-01 | 连云港东睦新材料有限公司 | Powder metallurgy friction material and preparation method and application thereof |
| CN117144183B (en) * | 2023-09-13 | 2024-03-15 | 连云港东睦新材料有限公司 | Powder metallurgy friction material and preparation method and application thereof |
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