CN1541280A - Sintered alloy, method for prodn. thereof and valve sheet - Google Patents
Sintered alloy, method for prodn. thereof and valve sheet Download PDFInfo
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- CN1541280A CN1541280A CNA028137493A CN02813749A CN1541280A CN 1541280 A CN1541280 A CN 1541280A CN A028137493 A CNA028137493 A CN A028137493A CN 02813749 A CN02813749 A CN 02813749A CN 1541280 A CN1541280 A CN 1541280A
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- 238000005245 sintering Methods 0.000 claims description 39
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- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 20
- 229910052799 carbon Inorganic materials 0.000 claims description 15
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- 229910017052 cobalt Inorganic materials 0.000 description 3
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- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
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Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0207—Using a mixture of prealloyed powders or a master alloy
-
- 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
-
- 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
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
Abstract
Provided is a sintered alloy capable of showing wear resistance and a process for producing the same as well as a valve seat of good wear resistance. A sintered alloy comprising 4-30% by weight Mo, 0.2-3% by weight C, 1-30% by weight Ni, 0.5-10% by weight Mn, 2-40% by weight Co, and the balance of inevitable impurities and Fe when the entirety is taken as 100% by weight. Aprocess for producing a sintered alloy in which a green compact of a raw mixture powder including hard particles is sintered, thereby producing said sintered alloy. A valve seat comprising said sintered alloy.
Description
Technical field
The present invention relates to the good sintered alloy of wear resistance, be used to prepare the method for this alloy, and the valve seat that contains the good sintered alloy of wear resistance.
Background technology
Being used for motor car engine or suchlike oil engine is equipped with and is used for air-breathing and deflated valve and the valve seat that valve is disposed thereon.
Valve seat is required to have high wear resistance.In case valve seat is worn, will when falling on the valve seat, valve produce the problem of valve seat recession.
As the valve seat of high abrasion resistance, for example can use by Co base hard particles and be dispersed in sintered alloy in the Fe base alloy substrate.In addition, the open communique spy of Japan's special permission opens flat 9-242516 and discloses the valve seat that a kind of oil engine is used.
It is a kind of oil engine valve seat that the open communique spy of Japan's special permission opens the disclosed valve seat of flat 9-242516, wherein, the cobalt-based hard particles is dispersed in the matrix of Fe base alloy, it is characterized in that, in matrix as matrix components, at least contain C:0.5-1.5 weight % and at least a element that is selected among Ni, Co and the Mo: its total amount is the Fe of 2.0-20.0 weight % and surplus, and the amount of contained cobalt-based hard particles is 26-50 weight % simultaneously.
Yet, when this valve seat is used as the valve seat of gas engine, have the imperfect problem of wear resistance.
Using liquid fuel for example in the engine of gasoline and light oil, keep the lubricity between valve and the valve seat by fuel or products of combustion (for example C), and this lubricity can prevent the prooving of valve seat.
Natural gas liquids) and compressed natural gas (CNG: in engine compressed natural gas), on the other hand, at using gas fuel liquefied petroleum gas (LPG) (LPG: for example because the products of combustion that produces is less, so can not fully guarantee the lubricity between valve and the valve seat.
In addition, in gas engine, because the reductive action of the hydrogen that comprises in a large number in fuel gas, unlikely being formed with on the slipping plane of valve seat helps oxide film lubricated between the solid.
Summary of the invention
The present invention be directed to these situations finishes.That is to say, the purpose of this invention is to provide a kind of method and good valve seat of wear resistance that can show the sintered alloy of abundant wear resistance and be used to prepare this alloy.
In order to solve this problem, the inventor has carried out deep research and has repeated the experiment of various different systems, the result, a class sintered alloy and thing like that have been developed, their hardness increases density by the diffusion that promotes Mn when the sintering and is improved, simultaneously, Mo forms oxide film therein, and this oxide film has guaranteed the solid lubricity.
Sintered alloy of the present invention is when containing during as 100 weight % with its total amount: the Mo of 4-30 weight %; 0.2-3 the C of weight %; The Ni of 1-30 weight %; 0.5-10 the Mn of weight %; The Co of 2-40 weight %; And surplus is unavoidable impurities and Fe.
Preferably, when total amount with 100 weight % timing, it can contain at least a composition among 5 weight % or Cr still less and 2 weight % or the Si still less.
Preferably, this alloy can have the tissue that is dispersed with the hard phase in matrix.
A kind of method that is used to prepare sintered alloy of the present invention comprises the steps: to prepare a kind of mixed powder of being made up of hard-particle powder, carbon dust, Co powder and Fe powder or low alloy steel powder, wherein, when with the total amount of above-mentioned hard-particle powder during as 100 weight %, this hard-particle powder contains: the Ni of the Mo of 20-60 weight %, 3 weight % or C still less, 5-40 weight %, the Mn of 1-20 weight %, the Co of 5-40 weight %, surplus are unavoidable impurities and Fe; When with the total amount of above-mentioned mixed powder during as 100 weight %, this mixed powder contains: hard-particle powder 10-60 weight %, carbon dust 0.2-2 weight %, Co powder 20 weight % or still less, surplus is Fe powder or low alloy steel powder; This mixed powder mold pressing is become the briquetting blank; With this briquetting blank sintering, make a kind of sintered alloy thus with each described composition among the claim 1-2.
Preferably, when with the total amount of above-mentioned mix powder during as 100 weight %, this mix powder can contain the Ni powder by 10 weight % or mixed still less.
Preferably, when with the total amount of above-mentioned hard-particle powder during as 100 weight %, this hard particles can contain at least a composition among the Si of the Cr that is selected from 10 weight % or smaller scale and 4 weight % or smaller scale.
Valve seat of the present invention is when containing during as 100 weight % with its total amount: Co and the surplus of Mn, the 2-40 weight % of the C of the Mo of 4-30 weight %, 0.2-3 weight %, the Ni of 1-30 weight %, 0.5-10 weight % are unavoidable impurities and Fe.
Preferably, when with the total amount of above-mentioned valve seat during as 100 weight %, it can contain at least a composition that is selected among 5 weight % or Cr still less and 2 weight % or the Si still less.
Preferably, this valve seat has the tissue that is dispersed with the hard phase in matrix.
It should be noted that in the present invention the weight percent that indicates the proportion of composing of coherent element is equal to mass percent.
Description of drawings
Fig. 1 is the equipment configuration synoptic diagram that long duration test of the present invention is carried out in explanation.
Optimum implementation of the present invention
Below, will invention and the specific embodiment of the present invention that the present invention is specialized be described.
Embodiments of the present invention
[sintered alloy]
Sintered alloy of the present invention is when containing during as 100 weight % with its total amount: the Mo of 4-30 weight %; 0.2-3 the C of weight %; The Ni of 1-30 weight %; 0.5-10 the Mn of weight %; The Co of 2-40 weight %; And surplus is unavoidable impurities and Fe.
Sintered alloy of the present invention is owing to increase density by the diffusion that promotes Mn when sintering, thereby hardness is improved, and simultaneously because Mo forms oxide film, thereby guaranteed the solid lubrication performance that produced by oxide film.
In sintered alloy of the present invention, Mo is that a kind of Mo of formation carbide is to improve the element of sintered alloy hardness and wear resistance.In addition, sintered alloy of the present invention disperses owing to sintering makes and the Mo of solid solution in tissue and the oxide film of Mo carbide formation Mo, and this oxide film has improved the solid lubrication performance.
And when Mo was less than 4 weight %, it is insufficient that Mo becomes, so that the formation of oxide film becomes insufficient, and can not obtain the solid lubrication performance at last.In addition, when Mo surpasses 30 weight %, excessively form oxide film, cause oxide film to peel off.Oxide film peel off the reduction that has caused sintered alloy hardness and wear resistance.In addition, when Mo surpasses 30 weight %, can cause the material productive rate when preparation is used to form the raw material powder of sintered alloy to reduce.In order to prepare raw material powder, can use for example such method of atomization.
C is a kind of element that forms the Mo carbide and therefore improve sintered alloy hardness and wear resistance that combines with Mo.When C was less than 0.2 weight %, the amount that the Mo carbide forms was so few, so that make wear resistance become insufficient.In addition, when C surpassed 3 weight %, the density of sintered alloy reduced.
Ni is the element that a kind of austenite that the solid solution capacity that causes Mo is improved increases mutually.That is, when Ni improves the solid solution capacity of Mo, can improve the wear resistance of sintered alloy.When Ni was less than 1 weight %, the solid solution capacity of Mo was so few, so that can not obtain sufficient abrasion resistance.When Ni surpassed 30 weight %, sintered alloy hardness reduced.
Because Mn can spread when sintering effectively, improve so it is a kind of adhesivity that constitutes the sintered alloy tissue that makes, and therefore make the element of the density raising of sintered alloy.In addition, because Mn has the effect that austenite is increased mutually, therefore, it can improve wear resistance by the solid solution capacity that increases Mo.When Mn is less than 0.5 weight %, can not fully obtain the effect that density increases.In addition, when Mn surpassed 10 weight %, above-mentioned effect (effect that density improves) had reached saturated.
Co is a kind of element that makes austenite in the sintered alloy increase and improve simultaneously hardness mutually.When the Co amount is less than 2 weight %, can not observe the effect of adding Co, when Co surpassed 40 weight %, the effect of above-mentioned (austenite phase and hardness increase) had reached saturated.
Preferably, sintered alloy of the present invention is when during as 100 weight %, also containing at least a composition that is selected from 5 weight % or chromium still less (Cr) and 2 weight % or the silicon still less (Si) with its total amount.Be noted that, to Cr be 5 weight % or still less and to Si be 2 weight % or still less both the regulation scopes do not comprise 0 weight %.
Cr is the excessive formation oxide film of a kind of Mo of inhibition, thereby prevents the element that the sintered alloy wear resistance reduces.That is, when for example being exposed to high temperature, can form oxide film in large quantities on sintered alloy, the oxide film that causes generating is peeled off, thereby causes the sintered alloy wearing and tearing.It has been known that Cr demonstrates high oxidation starting temperature.When adding Cr, the generation of oxide compound is suppressed in sintered alloy, has therefore prevented the reduction of sintered alloy wear resistance.In addition, when Cr surpassed 5 weight %, the growing amount of oxide compound (oxide film) became so few, so that the solid lubrication performance of sintered alloy is reduced.
Si is the adhering element of a kind of raising oxide film.In addition, when Si surpasses 2 weight %, density is reduced, thereby cause sintered alloy hardness to reduce.
Preferably, sintered alloy of the present invention has and a kind ofly is scattered in the tissue that forms in the matrix mutually by hard.The dispersive hard can improve the hardness of matrix mutually in matrix, thereby improves its wear resistance.
By being incorporated in sintering under this state, can make the hard phase mixing at the hard particles that is transformed into the hard phase behind the sintering.Because the element that takes place between hard particles that produces and the matrix moves, therefore can not clearly determine the composition of hard phase when sintering.
Preferably, before sintering hard particles as the Co of Mn, the 5-40 weight % of Ni, the 1-20 weight % of the Mo, the 3 weight % that contain 20-60 weight % with the particulate total amount during as 100 weight % or C still less, 5-40 weight % and the unavoidable impurities and the Fe of surplus.
[preparation method of sintered alloy]
The preparation method of sintered alloy of the present invention is a kind of by will be by the mix powder mold pressing of the powder of hard-particle powder and matrix forming element and the preparation method that sintering makes the sintered alloy of claim 1-2 defined.
Preparation method of the present invention at first prepares a kind of mix powder of being made up of hard-particle powder, carbon dust, cobalt (Co) powder and Fe powder or low alloy steel powder.
In the sintered alloy that makes by sintering, hard particles has constituted the hard phase that can improve wear resistance.When hard particles was less than 10 weight %, the amount of hard phase became insufficient in the sintered alloy that makes, so that can not produce the effect that wear resistance improves.When hard particles surpassed 60 weight %, the sintered alloy that makes lacked bond strength.In addition, when hard particles is excessive, strengthened the aggressiveness of sintered alloy, can not guarantee that hard particles is deposited in the sintered alloy that makes simultaneously for kit.
Carbon (C) element that constitutes carbon dust when sintering, spread or solid solution in the matrix (Fe or low alloy steel) or hard particles of sintered alloy, or generation carbide (Mo carbide).As carbon dust, the suitable Graphite Powder 99 that uses.When carbon dust is less than 0.2 weight %, in the matrix of the sintered alloy that makes, there is more ferritic phase.The increase of ferritic phase has reduced the hardness of matrix, reduces the wear resistance of sintered alloy thus.When carbon dust surpasses 2 weight %, in sintered alloy, there is more cementite phase, make sintered alloy toughness reduce.
The Co powder increases the density that makes sintered alloy.When the Co powder surpassed 20 weight %, the effect that sintered alloy density is increased had reached saturated.Notice that the scope of " Co powder ratio be 20 weight % or still less " indication does not comprise 0 weight %.
Fe powder or low alloyed steel powder form the matrix of sintered alloy.As the low alloy steel powder, can use the Fe-C powdered alloy.For example, when during as 100 weight %, using powdered alloy: the C of 0.2-5 weight %, and the unavoidable impurities of surplus and Fe with following composition with the low alloy steel powder.
Simultaneously, above-mentioned hard particles is when containing during as 100 weight % with its total amount: the Mo of 20-60 weight %; 3 weight % or C still less; The Ni of 5-40 weight %; The Mn of 1-20 weight %; The Co of 5-40 weight %; And the unavoidable impurities of surplus and Fe.
Mo in the hard particles combines with C and forms the Mo carbide, is formed on the good hard in hardness and wear resistance aspect thus mutually.When Mo was less than 20 weight %, it is insufficient that Mo becomes, so that the formation of oxide film is insufficient and can not obtain enough solid lubrication performances.In addition, when Mo surpasses 60 weight %, in the sintered alloy that makes, excessively form oxide film, and cause this oxide film to be peeled off, so that the hardness of sintered alloy and wear resistance are reduced.In addition, when Mo surpassed 30 weight %, the material productive rate by preparation hard-particle powders such as atomizations the time reduced.
C in the hard particles combines with Mo and forms the Mo carbide, is formed on the good hard in hardness and wear resistance aspect thus mutually.When C surpassed 3 weight %, the density that makes sintered alloy reduced.Note,, also can form the hard phase thus owing to diffusion makes C and Mo form the Mo carbide from the carbon dust in the mix powder even the C in hard particles exists more after a little while.Notice that in preparation method of the present invention, hard particles contains C.That is, be defined in that C content 3 weight % are illustrated in greater than in 0 weight % to 3 weight % or the scope still less in the hard particles.
Ni in the hard particles has increased the austenite phase of the solid solution capacity raising that can make Mo, is formed on the good hard phase in wear resistance aspect thus.When Ni was less than 5 weight %, the meltage of Mo was insufficient, so that can not obtain enough wear resistancies.In addition, when Ni surpassed 40 weight %, hardness reduced.
Because the Mn in the hard particles is a kind of element that can effectively diffuse into when sintering in the matrix, so it can improve the adhesivity between matrix and the hard particles, thereby has improved the density of sintered alloy.In addition, because Mn has the effect that austenite is increased mutually, therefore improved wear resistance.As Mn during less than 1 weight %, can not fully reach the effect that improves density, when Mn surpassed 20 weight %, above-mentioned effect had reached saturated.
Co in the hard particles can make the austenite in the hard particles increase mutually, and improves hardness simultaneously.When Co is less than 5 weight %, can not observe the effect (austenite phase and hardness increase) of adding Co, when Co surpassed 40 weight %, above-mentioned effect (austenite phase and hardness increase) had reached saturated.
Preferably, when during as 100 weight %, in this mixture, advancing the Ni powder by 10 weight % or mixed still less with the total amount of mix powder.Note, 10 weight % or still less the scope of indication do not comprise 0 weight %.That is, when the Ni pruinescence is mixed into mix powder, when sintering, can promote elemental diffusion, thereby can improve the density of sintered alloy.In addition, when the ratio of Ni powder surpassed 10 weight %, the residual austenite in matrix increased mutually, thereby caused the wear resistance of the sintered alloy that makes to reduce.
Preferably, when with the total amount of hard-particle powder during as 100 weight %, this hard particles can contain at least a composition that is selected among 10 weight % or Cr still less and 4 weight % or the Si still less.Note, 10 weight % or still less with 4 weight % or still less the scope of both indications do not comprise 0 weight %.
Cr is that a kind of Mo of preventing excessively forms oxide film and therefore prevents the element that the sintered alloy wear resistance reduces.That is, when for example being exposed in the high temperature sometimes, on sintered alloy, can form oxide film in a large number.The oxide film that generates is peeled off, thereby causes the wearing and tearing of alloy.Cr shows that high oxidation starting temperature this point is known.When adding Cr, the oxide compound in the sintered alloy generates and is suppressed, thereby has prevented the reduction of sintered alloy wear resistance.In addition, when Cr surpassed 10 weight %, the quantitative change of generation oxide compound (oxide film) got so few, so that make the solid lubrication reduction.
Si is the adhering element of a kind of raising oxide film.In addition, when Si surpassed 4 weight %, density reduced and sintered alloy hardness is reduced.
Preferably, the preparation method of sintered alloy of the present invention carries out temper after with briquetting blank sintering.That is, when sintered alloy was carried out tempering, the matrix of sintered alloy all became stable with hard crystal structure mutually.
Preferably, the preparation method of sintered alloy of the present invention carries out conducting forging processing after with briquetting blank sintering.When sintered alloy is forged, can not only make the shape of sintered alloy become required shape, and can remove the hole that produces by sintering, and therefore can improve the density and the wear resistance of sintered alloy.
The preparation method of sintered alloy of the present invention can be used to reduce material cost.In addition, can also improve the compressed moulding of briquetting blank.And, can not only make the briquetting blank, and can make the sintered alloy densification.
The preparation method of sintered alloy of the present invention comprises, makes the element mutual diffusion mutually that is comprised in hard particles and the matrix when sintering.Elemental diffusion makes the adhesivity between hard particles and the matrix strengthen.Specifically, because the Mn that is comprised in the hard particles diffuses in the matrix effectively, therefore strengthened the adhesivity between hard particles and the matrix.Thereby the density of sintered alloy is improved, and the hardness of sintered alloy and wear resistance are improved.
In the preparation method of sintered alloy of the present invention, the preparation method of hard particles is not particularly limited.As the preparation method of hard particles, for example can enumerate to handle and prepare the particulate method by the atomizing that molten metal is sprayed, obtain the particulate method solidifying the curing material that obtains with mechanical disintegration by the deposite metal.As for the atomizing treatment process, can use in non-oxidizing atmosphere those methods of (inert gas atmosphere, for example nitrogen and argon gas, or in a vacuum) atomizing.
In addition, about the median size of hard particles, can carry out appropriate selection according to the purposes of the sintered alloy that makes, type etc., yet that preferable can be about 20-250 μ m usually, about 30-200 μ m and about 40-180 μ m.But the median size of hard particles is not limited to these scopes.
In addition, the hardness of hard particles depends on the amount of Mo carbide etc., still, can be about Hv350-750 and about Hv450-700 usually.Yet the hardness of hard particles is not limited to these scopes, as long as the hard particles in the sintered alloy matrix is harder than using object.
In the preparation method of sintered alloy of the present invention,, can adopt about 1050-1250 ℃, particularly about 1100-1150 ℃ as sintering temperature.As the sintering time under above-mentioned sintering temperature, can adopt particularly 45-90 minute 30-120 minute.In addition, about sintering atmosphere, be preferably nonoxidizing atmosphere, for example inert gas atmosphere.As nonoxidizing atmosphere, can enumerate nitrogen atmosphere, argon atmospher and vacuum atmosphere.
Because the preparation method of sintered alloy of the present invention carries out sintering by hard particles, carbon dust, Co powder and Fe alloy powder are mixed, and has therefore promoted elemental diffusion in hard particles and the matrix in sintering, and the density of the sintered alloy that makes is improved.In addition, owing to promoted elemental diffusion, thus make Mo spread in large quantities.The Mo of this diffusion forms carbide and oxide film, and therefore makes sintered alloy all obtain to improve in wear resistance and solid lubrication aspect of performance.
[valve seat]
Valve seat of the present invention is when containing during as 100 weight % with its total amount: the Mo of 4-30 weight %; 0.2-3 the C of weight %; The Ni of 1-30 weight %; 0.5-10 the Mn of weight %; The Co of 2-40 weight %; And the unavoidable impurities of surplus and Fe.
Mo is that a kind of Mo of formation carbide is to improve the element of valve seat hardness and wear resistance.In addition, disperse and the Mo of solid solution in tissue and the oxide film of Mo carbide formation one deck Mo by sintering, the oxide film that is obtained has improved the solid lubrication performance of valve seat.
When Mo is 4 weight % or still less the time, it is insufficient that Mo becomes, thereby make the formation of oxide film insufficient and can not obtain enough solid lubrication performances at last.In addition, when Mo surpasses 30 weight %, exceedingly form oxide film, the result causes peeling off of oxide film, and reduces the wear resistance of valve seat.In addition, when Mo surpasses 30 weight %, be used to form in the technology of raw material powder of valve seat, cause the material productive rate to reduce in preparation.As for the preparation of raw material powder, atomization etc. is for example arranged.
C is that a kind of can the combination with Mo forms the element that therefore the Mo carbide also improves hardness and wear resistance.When C is less than 0.2 weight %, thereby the very few wear resistance of valve seat that makes of amount that forms the Mo carbide becomes insufficient.In addition, when C surpassed 3 weight %, the density of valve seat reduced.
Ni is the element that a kind of austenite that the solid solution capacity that causes Mo is improved increases mutually.When Ni improves the solid solution capacity of Mo, can improve the wear resistance of valve seat.When Ni was less than 1 weight %, the solid solution capacity of Mo was so few, so that can not obtain sufficient abrasion resistance.In addition, when Ni surpassed 30 weight %, the effect that solid solution capacity increases had reached saturated.
Because Mn can spread when sintering effectively, thereby so it be a kind of element that can improve the adhesivity raising valve seat density that constitutes valve seat tissue.In addition, because Mn has the effect that austenite is increased mutually, therefore can improve the wear resistance of valve seat by the solid solution capacity that increases Mo.When Mn is less than 0.5 weight %, can not fully obtain the effect that density is increased.In addition, when Mn surpassed 10 weight %, above-mentioned effect had reached saturated.
Co is a kind of element that can make austenite in the valve seat increase and improve simultaneously hardness mutually.When Co is less than 2 weight %, can not observe the effect that Co adds, when Co surpassed 40 weight %, above-mentioned effect had reached saturated.
Preferably, valve seat of the present invention is when during as 100 weight %, also containing at least a composition that is selected among 5 weight % or Cr still less and 2 weight % or the Si still less with its total amount.Note, to Cr be 5 weight % or still less and to Si be 2 weight % or still less both scopes of regulation do not comprise 0 weight %.
Cr is the excessive formation oxide film of a kind of Mo of inhibition, thereby prevents the element that the valve seat wear resistance reduces.That is, when for example being exposed to high temperature, on valve seat, can form oxide film in large quantities.The oxide film that generates is peeled off, thereby causes the wearing and tearing of valve seat.It has been known that Cr demonstrates high oxidation starting temperature.When adding Cr, the generation of oxide compound is suppressed on valve seat, has therefore prevented the reduction of valve seat wear resistance.In addition, when Cr surpassed 5 weight %, the growing amount of oxide compound (oxide film) became so few, so that the solid lubrication performance of valve seat is reduced.
Si is the adhering element of a kind of raising oxide film.In addition, when Si surpasses 2 weight %, density is reduced, thereby cause valve seat hardness to reduce.
Preferably, valve seat of the present invention has and a kind ofly is scattered in the tissue that forms in the matrix mutually by hard.Valve seat of the present invention is brought into play its wear resistance mutually by the hard that is scattered in the matrix.
Valve seat of the present invention can make by the preparation method of claim 3-5 defined.That is, when by with hard particles, carbon dust, Co powder with the Fe powdered alloy mixes and when its sintering made valve seat, owing to when sintering, promoted hard particles and matrix elemental diffusion, so can improve the density of valve seat.In addition, owing to promoted elemental diffusion, and therefore Mo is spread in a large number, and the Mo formation carbide and the oxide film that should spread, therefore form a kind of wear resistance and all good valve seat of solid lubrication performance.
Because valve seat of the present invention has improved density and has improved solid lubrication effect from oxide film simultaneously, therefore can become a kind of valve seat that possesses high-wearing feature, even also can demonstrate enough wear resistancies when using it for gas engine.
Embodiment
The various different embodiment that enumerate relevant sintered alloy of the present invention, the method for preparing this alloy and valve seat below are described more specifically the present invention.
(preparation of hard particles)
In the present embodiment, prepare the powder that sample " A "-" R " with table 1 defined forms by carry out gas atomization with rare gas element (nitrogen).In addition, after fusing, prepare " S " powdered alloy formed that has sample by pulverizing.These powdered alloys are sieved into the powder of 44-180 mu m range, and used as hard particles.
Table 1
Cited sample " A "-" J " of table 1 is the powder corresponding to preparation method's hard particles of the present invention.Sample " K " is corresponding to control sample, because Mo has only 15 weight %.Sample " L " does not comprise the good Mn of diffuser efficiency, corresponding to control sample.Sample " M " because its C content is slightly high, is 3.5 weight % corresponding to control sample.Sample " N " because its Ni content is slightly high, is 45 weight % corresponding to control sample.Sample " O " because wherein contain a large amount of Cr, is 15 weight % corresponding to control sample.Sample " P " because its Si content is slightly high, is 5% corresponding to control sample.Sample " Q " is corresponding to control sample, because Co has only 2 weight % few like this.Sample " R " is corresponding to control sample, because it is not contain Mn and Co and contain the slightly high Ni base alloy of Cr amount.Sample " S " is traditional sample, because it is molybdenum-iron (FeMo) and does not conform to Ni and Mn.
| Composition (weight %) | Oxidation starting temperature (℃) | |||||||||
| ??Mo | ??C | ??Ni | ????Mn | ??Co | ????Cr | ??Si | Fe | |||
| ??A | ??33 | ??0.9 | ??10 | ????6 | ??30 | Surplus | ??630 | The present invention | ||
| ??B | ??33 | ??0.9 | ??10 | ????6 | ??30 | ????4 | Surplus | ??650 | ||
| ??C | ??33 | ??0.9 | ??10 | ????6 | ??30 | ????4 | ??0.8 | Surplus | ??660 | |
| ??D | ??23 | ??0.9 | ??10 | ????6 | ??30 | ????4 | ??0.8 | Surplus | ??670 | |
| ??E | ??60 | ??0.9 | ??10 | ????6 | ??30 | ????4 | ??0.8 | Surplus | ??640 | |
| ??F | ??33 | ??0.9 | ??10 | ????1.5 | ??30 | ????4 | ??0.8 | Surplus | ??650 | |
| ??G | ??33 | ??0.9 | ??10 | ????18 | ??30 | ????4 | ??0.8 | Surplus | ??650 | |
| ??H | ??33 | ??2.5 | ??10 | ????6 | ??30 | ????4 | ??0.8 | Surplus | ??670 | |
| ??I | ??33 | ??0.9 | ??6 | ????6 | ??30 | ????4 | ??0.8 | Surplus | ??650 | |
| ??J | ??33 | ??0.9 | ??35 | ????6 | ??15 | ????4 | ??0.8 | Surplus | ??670 | |
| ??K | ??15 | ??0.9 | ??10 | ????6 | ??30 | ????4 | ??0.8 | Surplus | ??750 | Control sample |
| ??L | ??33 | ??0.9 | ??10 | ??30 | ????4 | ??0.8 | Surplus | ??650 | ||
| ??M | ??33 | ??3.5 | ??10 | ????6 | ??30 | ????4 | ??0.8 | Surplus | ??680 | |
| ??N | ??33 | ??0.9 | ??45 | ????6 | ??10 | ????4 | ??0.8 | Surplus | ??690 | |
| ??O | ??33 | ??0.9 | ??10 | ????6 | ??30 | ????15 | ??0.8 | Surplus | ??780 | |
| ??P | ??33 | ??0.9 | ??10 | ????6 | ??30 | ????4 | ??5 | Surplus | ??730 | |
| ??Q | ??34 | ??0.8 | ??9 | ????6 | ??2 | ????4 | ??0.8 | Surplus | ??640 | |
| ??R | ??25 | ??3 | Surplus | ????20.5 | ??1.1 | 17.3 | ??900 | |||
| ??S | ??63 | ??1.1 | Surplus | ??580 | ||||||
Use the hard-particle powder of these samples of " A "-" S ", in air, various hard-particle powders are heated so that its oxidation, measure and to follow oxidation in this case and temperature when making weight begin to increase suddenly, and with this temperature as oxidation starting temperature.Table 1 has been listed the whole oxidation starting temperatures that record.
As described in Table 1, in hard particles sample " A "-" J " corresponding to preparation method's regulation of the present invention, oxidation starting temperature is about 630-670 ℃, and this oxidation starting temperature is lower.The low just expression of oxidation starting temperature, when it was used as sintered alloy, the oxide film that plays the effect of solid lubrication performance just began to form in lower temperature range.That is, so-called oxide film just begins to form in lower temperature range, is meant that oxide film forms easily, and expression, can form the oxide film that has q.s for the solid lubrication performance.
(preparation of sintered alloy)
With the listed ratio of table 2, with hard-particle powder, powdered graphite, the particle diameter of said sample " A "-" S " is that Ni powder, the particle diameter of 2-60 μ m is that Co powder and the particle diameter of 4-100 μ m is that 150 μ m or littler pure Fe powder mix with mixing machine, thereby forms the mixed powder as mixing material.As listed in the table 2, in most of embodiment, hard-particle powder is 40 weight %, and powdered graphite is 0.6 weight %, and the Ni powder is 6 weight %, and the Co powder is 6 weight %.
Notice that in embodiment 11, the ratio of hard-particle powder is reduced to 15%.In embodiment 12, the hard-particle powder ratio reaches 55%.In addition, in embodiment 13, the powdered graphite ratio is less slightly, is 0.3%.In embodiment 14, the powdered graphite ratio is slightly many, is 1.5%.In embodiment 15, do not add the Ni powder.In embodiment 16, not only do not add the Ni powder, and the Co proportion of powder is also slightly many, is 12%.In embodiment 17, do not add the Co powder.In embodiment 18, the ratio of Co powder is slightly many, is 12%.
Table 2
| Powdered alloy is formed (weight %) | ||||||||||||||||||||||
| ??A | ??B | ??C | ??D | ?E | ??F | ??G | ??H | ??I | ??J | ????L | ?M | ?N | ????O | ????P | ?Q | ?R | Graphite Powder 99 | The Fe powder | The Ni powder | The Co powder | ||
| Embodiment #1 | ??40 | ??0.6 | Surplus | ????6 | ????6 | |||||||||||||||||
| Embodiment #2 | ??40 | ??0.6 | Surplus | ????6 | ????6 | |||||||||||||||||
| Embodiment #3 | ??40 | ??0.6 | Surplus | ????6 | ????6 | |||||||||||||||||
| Embodiment #4 | ??40 | ??0.6 | Surplus | ????6 | ????6 | |||||||||||||||||
| Embodiment #5 | ?40 | ??0.6 | Surplus | ????6 | ????6 | |||||||||||||||||
| Embodiment #6 | ??40 | ??0.6 | Surplus | ????6 | ????6 | |||||||||||||||||
| Embodiment #7 | ??40 | ??0.6 | Surplus | ????6 | ????6 | |||||||||||||||||
| Embodiment #8 | ??40 | ??0.6 | Surplus | ????6 | ????6 | |||||||||||||||||
| Embodiment #9 | ??40 | ??0.6 | Surplus | ????6 | ????6 | |||||||||||||||||
| Embodiment #10 | ??40 | ??0.6 | Surplus | ????6 | ????6 | |||||||||||||||||
| Embodiment #11 | ??15 | ??0.6 | Surplus | ????6 | ????6 | |||||||||||||||||
| Embodiment #12 | ??55 | ??0.6 | Surplus | ????6 | ????6 | |||||||||||||||||
| Embodiment #13 | ??40 | ??0.3 | Surplus | ????6 | ????6 | |||||||||||||||||
| Embodiment #14 | ??40 | ??1.5 | Surplus | ????6 | ????6 | |||||||||||||||||
| Embodiment #15 | ??40 | ??0.6 | Surplus | ????0 | ????6 | |||||||||||||||||
| Embodiment #16 | ??40 | ??0.6 | Surplus | ????0 | ????12 | |||||||||||||||||
| Embodiment #17 | ??40 | ??0.6 | Surplus | ????6 | ????0 | |||||||||||||||||
| Embodiment #18 | ??40 | ??0.6 | Surplus | ????6 | ????12 | |||||||||||||||||
| Embodiment #19 | ??40 | ??0.6 | Surplus | ????6 | ????6 | Forge behind the sintering | ||||||||||||||||
| Embodiment #20 | ??40 | ??0.6 | Surplus | ????6 | ????6 | 1,185 ℃ of sintering temperature | ||||||||||||||||
| Comparative Examples #1 | ????40 | ??0.6 | Surplus | ????6 | ????6 | |||||||||||||||||
| Comparative Examples #2 | ?40 | ??0.6 | Surplus | ????6 | ????6 | |||||||||||||||||
| Comparative Examples #3 | ?40 | ??0.6 | Surplus | ????6 | ????6 | |||||||||||||||||
| Comparative Examples #4 | ????40 | ??0.6 | Surplus | ????6 | ????6 | |||||||||||||||||
| Comparative Examples #5 | ????40 | ??0.6 | Surplus | ????6 | ????6 | |||||||||||||||||
| Comparative Examples #6 | ?40 | ??0.6 | Surplus | ????6 | ????6 | |||||||||||||||||
| Comparative Examples #7 | ?40 | ??0.6 | Surplus | ????6 | ????6 | |||||||||||||||||
| Comparative Examples #8 | ??7 | ??0.6 | Surplus | ????6 | ????6 | |||||||||||||||||
| Comparative Examples #9 | ??70 | ??0.6 | Surplus | ????6 | ????6 | |||||||||||||||||
| Comparative Examples #10 | ??40 | ??0.1 | Surplus | ????6 | ????6 | |||||||||||||||||
| Comparative Examples #11 | ??40 | ??2.5 | Surplus | ????6 | ????6 | |||||||||||||||||
| Comparative Examples #12 | ??40 | ??0.6 | Surplus | ????12 | ????6 | |||||||||||||||||
| Comparative Examples #13 | ??40 | ??0.6 | Surplus | ????0 | ????0 | |||||||||||||||||
Then, by using shaping mould, above-mentioned blended mix powder is applied 78.4 * 10
7Handkerchief (8 ton forces/cm
2) pressure is shaped to the annular test block with it, forms the briquetting blank thus.This test block has the valve seat shape.
Then,, and carried out tempering 100 minutes, form sintered alloy (valve seat) thus as test block at 600 ℃ with sintering in the inert atmosphere (nitrogen atmosphere) of each briquetting blank under 1150 ℃ 45 minutes.
Notice that embodiment 19 is with 137.2 * 10 behind sintering
7(14 tons/cm of handkerchiefs
2) pressure forges, and then carries out tempering 100 minutes at 600 ℃.In addition, embodiment 20 carries out sintering under 1185 ℃ of sintering temperatures.
In addition, in Comparative Examples 1-13, equally with its compressed moulding for having the annular test block, make sintered alloy (valve seat) thus as test block.
In addition, according to the listed condition of table 3, in Comparative Examples 14 and 15, similarly make sintered alloy (valve seat) as test block.Note, in table 3, not only listed whole compositions of sintered alloy, and listed hard particles sample and blending ratio thereof.
As listed in the table 3, Comparative Examples 14 has used sample " S " as hard particles, and with briquetting blank sintering, this briquetting blank is to mix the mix powder extrusion forming that forms by handle with the sample " S " of 10 weight % to make.Comparative Examples 15 has used sample " R " as hard particles, and with briquetting blank sintering, and this briquetting blank is to make by the mix powder extrusion forming that handle and 20% sample mixed form.
Table 3
| Composition (weight %) | The hard-particle powder type | Hard particles ratio (weight %) | ||||||||
| ?Mo | ?C | ?Ni | ?W | ?Co | ?Cr | ?Si | ????Fe | |||
| Comparative Examples #14 | ?6.5 | ?0.4 | ?9.5 | ?0.8 | ?9.5 | Surplus | ????S | ????10 | ||
| Comparative Examples #15 | ?9 | ?1.5 | ?4 | ?2.5 | ?4 | ?4 | Surplus | ????R | ????20 | |
In addition, about sintered alloy, measure the density of sintered alloy and the hardness of sintered alloy respectively as embodiment and Comparative Examples test block.The sintered alloy hardness that records is macroscopical Vickers' hardness (load: 10Kgf).Table 4 has been listed these measurement results.
Table 4
| Sintered density (g/cm 3) | Sintered compact hardness (Hv10) | Wear resistance (mm) | Cutting tool abrasion loss (μ m) | ||
| ?200℃ | ?300℃ | ||||
| Embodiment #1 | ?7.34 | ?240 | ?0.2 | ?0.05 | ????50 |
| Embodiment #2 | ?7.32 | ?250 | ?0.15 | ?0.045 | ????55 |
| Embodiment #3 | ?7.35 | ?250 | ?0.15 | ?0.045 | ????48 |
| Embodiment #4 | ?7.32 | ?240 | ?0.2 | ?0.055 | ????46 |
| Embodiment #5 | ?7.37 | ?230 | ?0.15 | ?0.045 | ????55 |
| Embodiment #6 | ?7.3 | ?235 | ?0.22 | ?0.065 | ????50 |
| Embodiment #7 | ?7.36 | ?250 | ?0.13 | ?0.045 | ????60 |
| Embodiment #8 | ?7.3 | ?240 | ?0.21 | ?0.055 | ????55 |
| Embodiment #9 | ?7.32 | ?250 | ?0.18 | ?0.05 | ????50 |
| Embodiment #10 | ?7.34 | ?230 | ?0.2 | ?0.055 | ????65 |
| Embodiment #11 | ?7.14 | ?235 | ?0.15 | ?0.2 | ????62 |
| Embodiment #12 | ?7.3 | ?230 | ?0.2 | ?0.1 | ????50 |
| Embodiment #13 | ?7.35 | ?225 | ?0.2 | ?0.08 | ????55 |
| Embodiment #14 | ?7.3 | ?270 | ?0.2 | ?0.1 | ????65 |
| Embodiment #15 | ?7.32 | ?235 | ?0.19 | ?0.12 | ????67 |
| Embodiment #16 | ?7.35 | ?250 | ?0.15 | ?0.08 | ????72 |
| Embodiment #17 | ?7.32 | ?230 | ?0.1 | ?0.1 | ????50 |
| Embodiment #18 | ?7.37 | ?260 | ?0.15 | ?0.04 | ????60 |
| Embodiment #19 | ?7.8 | ?360 | ?0.07 | ?0.03 | ????82 |
| Embodiment #20 | ?7.38 | ?260 | ?0.05 | ?0.04 | ????52 |
| Comparative Examples #1 | ?7.3 | ?230 | ?0.25 | ?0.25 | ????50 |
| Comparative Examples #2 | ?7.15 | ?240 | ?0.3 | ?0.2 | ????45 |
| Comparative Examples #3 | ?7.2 | ?250 | ?0.3 | ?0.2 | ????60 |
| Comparative Examples #4 | ?7.3 | ?200 | ?0.25 | ?0.25 | ????55 |
| Comparative Examples #5 | ?7.32 | ?270 | ?0.35 | ?0.05 | ????75 |
| Comparative Examples #6 | ?7.1 | ?230 | ?0.3 | ?0.2 | ????60 |
| Comparative Examples #7 | ?7.3 | ?240 | ?0.2 | ?0.2 | ????55 |
| Comparative Examples #8 | ?7.05 | ?210 | ?0.4 | ?0.5 | ????57 |
| Comparative Examples #9 | ?7.1 | ?180 | ?0.3 | ?0.25 | ????70 |
| Comparative Examples #10 | ?7.35 | ?200 | ?0.35 | ?0.15 | ????53 |
| Comparative Examples #11 | ?7.2 | ?270 | ?0.3 | ?0.2 | ????60 |
| Comparative Examples #12 | ?7.44 | ?200 | ?0.8 | ?0.1 | ????44 |
| Comparative Examples #13 | ?7.27 | ?215 | ?0.25 | ?0.12 | ????54 |
| Comparative Examples #14 | ?7 | ?200 | ?0.35 | ?0.3 | ????219 |
| Comparative Examples #15 | ?7 | ?230 | ?0.5 | ?0.06 | ????37 |
Below, by using the trier shown in Fig. 1, the wear resistance of sintered alloy is carried out wearing test, evaluate wear resistance thus.
In wearing test, as shown in Figure 1, use propane flammable gas burner 5, and the slipper as between the valve face 4 of the ring-shaped valve seats 3 of test block and valve 1 that the sintered alloy by embodiment and Comparative Examples forms is placed the propane flammable gas combustion atmosphere as heating source.The material of valve face 4 is SUH35.The temperature of valve seat 3 is controlled in 200 ℃, when valve seat 3 contacts with valve face 4, applies the load of 18Kgf by spring 6, and valve seat 3 is contacted with the frequency of valve face 4 by 2000 times/per minute, so carries out 8 hours wearing test.
In addition, be controlled at 300 ℃ occasion, carry out cut resistance test similarly in temperature with valve seat 3.Table 4 has been listed the abrasion loss when test temperature each test block when being 200 ℃ and 300 ℃.
Below, the processing characteristics of sintered alloy is estimated.
The evaluation of sintered alloy processing characteristics is carried out according to following method, promptly, is the ring-shaped valve seats of being made by embodiment and Comparative Examples sintered alloy that 0.05mm/ circle and joint-cutting are that the condition of 0.3mm is cut with cutter according to input speed, and measure the tool abrasion that causes by cutting, carry out the evaluation of sintered alloy processing characteristics then in view of the above, table 4 has been listed whole measurement results.
More detailed test method is that at first the axle core along peripheral direction around the valve seat annular mouth makes the valve seat rotation.At this moment, the inserted tool with Wimet H1 blade contacts with the inside circumference of ring-shaped valve seats end face.Then, mobile inserted tool, so that make, when along the circumferential direction rotation of the annular mouth of valve seat during 1 week, the blade that contacts with annular mouth foreign side radially moves 0.05mm.When inserted tool when moving with valve seat end face state of contact, the end face of valve seat just is cut.When cutting edge moves to the valve seat outside, it is turned back to the inside circumference of valve seat and proceeds similar cutting.At this moment, cutting edge axially returns 0.3mm inwardly along valve seat.When cutting is carried out 100 times, stop cutting, and measure the abrasion loss of cutter.
Can be clear that by table 4 sintered alloy of embodiment 1-20 is all good aspect density, hardness, wear resistance and processing characteristics.
On the other hand, equally at the sintered alloy of the listed Comparative Examples 1-15 of table 4 all inferior aspect density, hardness, wear resistance and the processing characteristics.
Below, with the valve seat of embodiment 3 and Comparative Examples 14 and 15 exhaust opening of engine one side of packing into.This engine uses white gasoline to act as a fuel, and has the cylinder displacement of 2400cc.And, use this engine to carry out long duration test in 180 hours.
In addition, the valve seat of embodiment 19 and Comparative Examples 13 is packed into inlet mouth one side of engine.This engine uses CNG to act as a fuel, and has the cylinder displacement of 1500cc.Use this engine to carry out long duration test in 300 hours.
Then, measure the overhang (mm) of valve and the increment (mm) of valve seat contact width respectively.As the condition of inlet mouth one side, valve face is a kind of SUH11 alloy that tufftride is handled that carried out thereon.As the condition of venting port one side, valve face is the SUH35 alloy.
The overhang of valve is meant, when valve closes, because the prooving of valve seat and valve face wearing and tearing cause the position of valve when valve closes to move the amount of (giving prominence to) outside engine.Valve seat contact width increment is meant because valve seat contacts with valve face, when causing the prooving of valve seat, in valve seat with the increment of the valve face contact part width of valve seat.Table 5 has been summarized these measuring results.
Table 5
| Suction opening | Venting port | ||||
| The overhang of valve (mm) | The increment of valve seat contact width (mm) | The overhang of valve (mm) | The increment of valve seat contact width (mm) | ||
| | Gasoline/180hr. | ??0.04 | ??0.4 | ||
| Comparative Examples #14 | Gasoline/180hr. | ??0.08 | ??0.6 | ||
| Comparative Examples #15 | Gasoline/180hr. | ??0.15 | ??0.7 | ||
| Embodiment #19 | ????CNG/300hr. | 0.05 | ?0.25 | ||
| Comparative Examples #13 | ????CNG/300hr. | 0.12 | ?0.6 | ||
As shown in table 5, as can be seen, be installed in the embodiment 3 of petrol engine exhaust side, to compare with 15 with Comparative Examples 14, the overhang of its valve and valve seat contact width increment all significantly reduce, and its high abrasion resistance.
In addition, also can find out, be installed in the embodiment 19 of gas-engine air inlet side, compare with Comparative Examples 13, the overhang of its valve and valve seat contact width increment significantly reduce, and its high abrasion resistance.
That is, be understood that the valve seat of being made by the embodiment sintered alloy has high hardness and good wear resistance.
Thereby because sintered alloy of the present invention has not only improved density, and has improved the solid lubrication performance from oxide film, so it has good wear resistance.
In addition, because the preparation method of sintered alloy of the present invention passes through with hard particles, carbon dust, Co powder and the mixing of Fe powdered alloy and with its sintering, therefore when sintering, promote elemental diffusion in hard particles and the matrix, and therefore improved the density of the sintered alloy that makes.In addition,, make Mo spread in large quantities, and, therefore make sintered alloy have good wear resistance and solid lubrication performance because the Mo of diffusion forms carbide and oxide film owing to promoted elemental diffusion.
In addition, owing to valve seat of the present invention is made by the sintered alloy of the present invention that the preparation method according to sintered alloy of the present invention makes, and, therefore has high wear resistance owing to the solid lubrication that has improved from oxide film.
Claims (9)
1. sintered alloy, when with its total amount during as 100 weight %, this alloy contains:
The Mo of 4-30 weight %;
0.2-3 the C of weight %;
The Ni of 1-30 weight %;
0.5-10 the Mn of weight %;
The Co of 2-40 weight %; And the unavoidable impurities of surplus and Fe.
2. sintered alloy as claimed in claim 1, described alloy is when contain at least a composition that is selected among 5 weight % or Cr still less and 2 weight % or the Si still less during as 100 weight % with its total amount.
3. the sintered alloy described in each of claim 1-2, this alloy has the tissue that is dispersed with the hard phase in matrix.
4. method that is used to prepare sintered alloy, this method comprises the steps:
Prepare a kind of mixed powder of forming by hard-particle powder, carbon dust, Co powder and Fe powder or low alloy steel powder, wherein, when the total amount with above-mentioned hard-particle powder was 100 weight %, this hard-particle powder contained: the Ni of the Mo of 20-60 weight %, 3 weight % or C still less, 5-40 weight %, the Co of the Mn of 1-20 weight %, 5-40 weight % and the unavoidable impurities and the Fe of surplus; When with the total amount of above-mentioned mixed powder during as 100 weight %, this mixed powder contains: the Fe powder or the low alloy steel powder of the carbon dust of the hard-particle powder of 10-60 weight %, 0.2-2 weight %, 20 weight % or Co powder still less and surplus;
With this mixed powder mold pressing to make the briquetting blank;
With this briquetting blank sintering to make a kind of sintered alloy with each described composition among the claim 1-3.
5. as being used to prepare the method for sintered alloy as described in the claim 4, wherein, when with the total amount of above-mentioned mix powder during as 100 weight %, this mix powder contains by 10 weight % or smaller scale blended Ni powder.
6. each described method for preparing sintered alloy among the claim 4-5, wherein, when with the total amount of above-mentioned hard-particle powder during as 100 weight %, this hard-particle powder contains at least a composition among the Si of the Cr that is selected from 10 weight % or smaller scale and 4 weight % or smaller scale.
7. valve seat, when with its total amount during as 100 weight %, this valve seat contains:
The Mo of 4-30 weight %,
0.2-3 the C of weight %,
The Ni of 1-30 weight %,
0.5-10 the Mn of weight %,
The Co of 2-40 weight % and the unavoidable impurities and the Fe of surplus.
8. valve seat as claimed in claim 7, when with its total amount during as 100 weight %, this valve seat contains at least a composition that is selected among 5 weight % or Cr still less and 2 weight % or the Si still less.
9. as each described valve seat among the claim 7-8, this valve seat has the tissue that is dispersed with the hard phase in matrix.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2001174885A JP4624600B2 (en) | 2001-06-08 | 2001-06-08 | Sintered alloy, manufacturing method thereof and valve seat |
| JP174885/2001 | 2001-06-08 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1541280A true CN1541280A (en) | 2004-10-27 |
| CN1284876C CN1284876C (en) | 2006-11-15 |
Family
ID=19016109
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN02813749.3A Expired - Lifetime CN1284876C (en) | 2001-06-08 | 2002-06-06 | Sintered alloy, method for prodn. thereof and valve sheet |
Country Status (7)
| Country | Link |
|---|---|
| US (1) | US20040194576A1 (en) |
| EP (1) | EP1405928B1 (en) |
| JP (1) | JP4624600B2 (en) |
| CN (1) | CN1284876C (en) |
| DE (1) | DE60228711D1 (en) |
| ES (1) | ES2314061T3 (en) |
| WO (1) | WO2002101107A1 (en) |
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| CN101952470B (en) * | 2008-02-20 | 2013-05-22 | 三菱制钢株式会社 | Powder for iron-based sintered alloy |
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| GB931961A (en) * | 1959-01-31 | 1963-07-24 | Birmingham Small Arms Co Ltd | Improvements in or relating to metal powders and articles produced therefrom |
| JPS56249A (en) * | 1979-06-13 | 1981-01-06 | Mazda Motor Corp | Hard-grain-dispersed sintered alloy for valve seat |
| JPS6244556A (en) * | 1985-08-21 | 1987-02-26 | Mitsubishi Metal Corp | High density sintered fe alloy having superior wear resistance and fitness |
| JP3191665B2 (en) * | 1995-03-17 | 2001-07-23 | トヨタ自動車株式会社 | Metal sintered body composite material and method for producing the same |
| JP2765811B2 (en) * | 1995-08-14 | 1998-06-18 | 株式会社リケン | Hard phase dispersed iron-based sintered alloy and method for producing the same |
| JP3614237B2 (en) * | 1996-02-29 | 2005-01-26 | 日本ピストンリング株式会社 | Valve seat for internal combustion engine |
| JP3469435B2 (en) * | 1997-06-27 | 2003-11-25 | 日本ピストンリング株式会社 | Valve seat for internal combustion engine |
| JP2970670B1 (en) * | 1998-02-25 | 1999-11-02 | トヨタ自動車株式会社 | Hardfacing alloys and engine valves |
| JP3596751B2 (en) * | 1999-12-17 | 2004-12-02 | トヨタ自動車株式会社 | Hard particle for blending sintered alloy, wear-resistant iron-based sintered alloy, method for producing wear-resistant iron-based sintered alloy, and valve seat |
-
2001
- 2001-06-08 JP JP2001174885A patent/JP4624600B2/en not_active Expired - Fee Related
-
2002
- 2002-06-06 DE DE60228711T patent/DE60228711D1/en not_active Expired - Lifetime
- 2002-06-06 US US10/479,848 patent/US20040194576A1/en not_active Abandoned
- 2002-06-06 WO PCT/JP2002/005632 patent/WO2002101107A1/en active IP Right Grant
- 2002-06-06 ES ES02733371T patent/ES2314061T3/en not_active Expired - Lifetime
- 2002-06-06 EP EP02733371A patent/EP1405928B1/en not_active Expired - Lifetime
- 2002-06-06 CN CN02813749.3A patent/CN1284876C/en not_active Expired - Lifetime
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Also Published As
| Publication number | Publication date |
|---|---|
| JP2002363681A (en) | 2002-12-18 |
| WO2002101107A1 (en) | 2002-12-19 |
| EP1405928A4 (en) | 2006-08-30 |
| EP1405928B1 (en) | 2008-09-03 |
| ES2314061T3 (en) | 2009-03-16 |
| CN1284876C (en) | 2006-11-15 |
| EP1405928A1 (en) | 2004-04-07 |
| DE60228711D1 (en) | 2008-10-16 |
| US20040194576A1 (en) | 2004-10-07 |
| JP4624600B2 (en) | 2011-02-02 |
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