CN1839006A - Mixed powder for powder metallurgy - Google Patents
Mixed powder for powder metallurgy Download PDFInfo
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- CN1839006A CN1839006A CN 200580000751 CN200580000751A CN1839006A CN 1839006 A CN1839006 A CN 1839006A CN 200580000751 CN200580000751 CN 200580000751 CN 200580000751 A CN200580000751 A CN 200580000751A CN 1839006 A CN1839006 A CN 1839006A
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Abstract
Disclosed is a mixed powder for powder metallurgy which is obtained by diffusing and adhering 0.05-1.0 mass% of Mo over the surface of an iron base powder which contains, as a prealloy, not more than 0.5 mass% of Mn and 0.2-1.5 mass% of Mo, thereby forming an alloy steel powder, and then blending 0.2-5 mass% of an Ni powder and/or 0.2-3 mass% of a Cu powder into the thus-formed alloy steel powder. A dense sintered body having excellent tensile strength and bending fatigue strength can be produced from such a mixed powder.
Description
Technical field
The present invention relates to mixed powder for powder metallurgy based on powdered alloy steel.The present invention be more particularly directed to be suitable for making the mixed powder for powder metallurgy of the various sintering metal parts that require good intensity.
Background technology
PM technique can reduce the cutting cost significantly with the parts of the shape extremely close with article shape (near net: simultaneously compound shape) production requirement high dimensional accuracy, complicated shape.Therefore, sintered metal product is as the parts of various machineries, device and utilize in many-side.
Generally speaking, alloy such as mixing graphite powder is with lubricant powders such as powder and stearic acid, lithium stearates and after forming the iron-based powder mixed powder in iron-based powder, this iron-based powder mixed powder is filled into metal die, press molding and make powder metallurgical with iron-based powder formed body (press-powder body).
Wherein, iron-based powder can be divided into iron powder (straight iron powder etc.), powdered alloy steel etc. according to composition.And iron-based powder also can be divided into atomized iron powder, reduced iron powder etc. according to manufacture method.
The density of iron-based powder formed body is generally 6.6～7.1Mg/m
3Further implement sintering processes and form sintered body for these iron-based powder formed bodies, and implement finishing, machining as required and form sintered metal product.And, when needing to improve hot strength, fatigue strength, also implement carburizing heat treatment, brightness heat treatment behind the sintering.
Recently, for miniaturization, the lightweight of parts, as the characteristic of the sintered metal product of iron class, strong request high strength, high-fatigue strength.
In order to improve the intensity of sintered metal product, generally in iron-based powder, add alloying element (Ni, Cu, Mo, W, V, Co, Nb, Ti etc.).
And, as the mode of adding alloying element, the mode that has the mode (prealloy) that makes the iron-based powder alloying, alloy is mixed together with powder (powder that contains desirable alloying element) and binding agent and iron-based powder, do not use binding agent and mode (diffusion is adhered to) that the mode of mixing and the powder that will contain alloying element and iron-based powder mixing afterwards combine in the high temperature maintenance and with metallurgical form.In each mode, differences such as the uniformity of alloying element, the disperse state when characteristic of each powdered alloy steel (or mixed powder), sintering.Therefore, the selection of alloying element and the selection of addition manner become the important factor of the quality of reaching target powdered alloy steel (or mixed powder), sintered body.
For example in the fair 6-89365 communique of spy, disclose a kind of powdered alloy steel, its ferrite stabilizer Mo of scope that comprises 1.5～20 quality % is as prealloy.And, when using this powdered alloy steel, in sintering circuit because to form the fast α of self diffusion velocity of Fe single-phase, thereby acceleration of sintering, it is the pore obturationization as a result, thereby can promote detailed-oriented by pressure sintering.And, can obtain homogeneous and stable tissue by the alloying element that does not use the diffusion attached type.But because the Mo addition is more than the 1.8 quality % and higher in reality open, and compressibility is low, thereby exists powder compact can not obtain the shortcoming of high density (formed body density).Therefore, can only obtain the goods of low frit density when using common sintering circuit (do not pressurize and once sintered), intensity, fatigue strength are insufficient.
And, owing to follow the double sintering method of pressure sintering method, recompression operation, the process cost height, thereby preferably, can not access high strength, high-fatigue strength as prerequisite with these special sintering process.
On the other hand, in the fair 7-51721 communique of spy, disclose that the scope with 0.2～1.5 quality % makes Mo pre-alloyed in iron powder, made the pre-alloyed comminuted steel shot of Mn with the scope of 0.05～0.25 quality %, the compressibility when its press-powder is shaped is higher.But, present inventors' latest find, because the Mo amount is below the 1.5 quality % in this comminuted steel shot, thereby it is mutually single-phase to form α.Thus, generally be used for the sintering temperature (1120～1140 ℃) of the meshbeltfurnace of powder used in metallurgy, owing to do not promote the carrying out of the sintering between the particle, thereby have the low problem of intensity of sintering neck.
And, in the fair 7-51721 communique of spy, though disclose the iron powder that Ni (3.8 quality %), Mo (0.5 quality %) and Cu (1.4 quality %) diffusion are adhered to as a comparative example, in this communique, put down in writing the result of the intensity variation after the disclosed above-mentioned powdered alloy steel heat treatment as inventing.
And in the public clear 63-66362 communique of spy, in the scope of not losing compression molding (Mo:0.1～1.0 quality %) that Mo is pre-alloyed in iron powder, Cu and Ni are adhered to and the compressibility when improving press-powder simultaneously and being shaped and the intensity of the parts behind the sintering with the powder type diffusion by particle surface at this iron powder.But because this technology and the disclosed technology of special fair 7-51721 communique are in the same manner, the agglutinating property of the iron powder of alloying is not so good in advance with Mo, thereby there are limit in the hot strength that causes of interpolation Cu and Ni and the raising of fatigue strength.
And open in the flat 8-49047 communique the spy, the prealloy amount that discloses Mn is suppressed at below the 0.3 quality %, by common interpolation (prealloy) Mo:0.1～6.0 quality % and V:0.05～2.0%, the sintered body after keeping compressibility and making heat treatment becomes high-intensity powdered alloy steel.And, can also in this powdered alloy steel, mix or spread to adhere to being selected from the Mo powder: below the 4 quality %, the Cu powder: below the 4 quality %, the Ni powder: below the 10 quality %, the Co powder: below the 4 quality % and the W powder: more than one in below the 4 quality %.
And, open in the flat 7-233401 communique the spy and to disclose the Mn that contains 0.03～0.5 quality % as prealloy, 0.03 the Cr of～less than 0.1 quality % etc., the atomized iron powder (powdered alloy steel) that machinability and dimensional accuracy are good, the intensified element that can be used as prealloy has been enumerated Ni (4.0 quality % are following), Mo (4.0 quality % are following), Nb (0.05 quality % is following), V (0.5 weight % following), and can enumerate Ni powder (5.0 quality % are following) as spreading the intensified element (alloyed powder) that adheres to, Mo powder (3.0 quality % are following) and Cu powder (5.0 quality % are following).
But, these technology have not been considered the alloy designs of the fatigue strength of the parts that obtain by sintering yet, thereby, even make the sintering metal parts, also be difficult to obtain the desired in recent years sintering metal parts that satisfy high-fatigue strength by common sintering circuit.
As with the improvement of fatigue strength powdered alloy steel, for example there is the spy to open flat 6-81001 communique, the spy opens the disclosed powdered alloy steel of 2003-147405 communique as purpose.
Open in the 2003-147405 communique the spy, disclose the powdered alloy steel that Mo:0.5～1.5 quality % diffusion is adhered to, used this powdered alloy steel and sintered body after can getable carburizing and quenching handling can obtain good face and presses fatigue strength.
And, open in the flat 6-81001 communique the spy, disclose at least a among Mo:0.05～2.5 quality % and V, Ti, the Nb is being contained in the iron-based powder as prealloy jointly, and the powdered alloy steel that Ni (0.5～5 quality %) and/or Cu (0.5～2.5 quality %) diffusion are adhered to, the sintered body after similarly carburizing and quenching is handled can obtain good face and press fatigue strength.
But, according to present inventors' discovery, to open in the 2003-147405 communique in the disclosed powdered alloy steel even open flat 6-81001 communique, spy the spy, the raising of the fatigue strength of sintered body (rotoflector fatigue strength) is also insufficient.
Summary of the invention
The present invention overcomes above-mentioned prior art problems, its purpose is to provide a kind of mixed powder for powder metallurgy, with powdered alloy steel as main body, wherein, do not utilize special sintering circuit can keep the density of higher sintered body yet, hot strength not only can be improved, bending fatigue strength can also be improved.
Mixed powder for powder metallurgy of the present invention adds the Ni powder: 0.2～5 quality % and Cu powder: any one among 0.2～3 quality % and forming at least in the powdered alloy steel that comprises the Mo:0.05～1.0 quality % that contain below the Mn:0.5 quality % as prealloy and adhere to powder type diffusion on the iron-based powder of Mo:0.2～1.5 quality % and the surface at this iron-based powder.
And, mixed powder for powder metallurgy of the present invention, in powdered alloy steel, add the Ni powder at least: 0.2～5 quality % and Cu powder: any one among 0.2～3 quality % and forming, wherein, there is more than 1% of area of section in Mo concentration on the surface of zone at above-mentioned powdered alloy steel more than the 2.0 quality %, below 30%, and, the surplus of this powdered alloy steel be Mo concentration more than 0.2 quality %, the zone of less than 2.0 quality %.
In addition, in the present invention, preferably, make at least a in above-mentioned Ni powder and the Cu powder by on the surface of binding agent attached to above-mentioned powdered alloy steel.
Description of drawings
Fig. 1 is the cutaway view that schematically shows the example of the powdered alloy steel that uses in the mixed powder for powder metallurgy of the present invention.
Fig. 2 is the calcspar of example that schematically shows the manufacturing process of the powdered alloy steel that uses in the mixed powder for powder metallurgy of the present invention.
Wherein, the implication of each label is as follows:
1: iron-based powder
2: contain Mo alloy powder (situation that comprises metal M o powder)
3: iron-based powder with contain the position that the Mo alloy powder contacts
4: powdered alloy steel
The specific embodiment
Below, further describe mixed powder for powder metallurgy of the present invention (powder that has promptly mixed powdered alloy steel and Ni powder, Cu powder) with reference to accompanying drawing.
At first, describe for powdered alloy steel.
As schematically showing among Fig. 1, be used in the particle of the powdered alloy steel 4 in the mixed powder for powder metallurgy of the present invention, contain Mo alloy powder 2 (below, metal M o powder also is considered as containing the Mo alloy powder) with position 3 that iron-based powder 1 contacts on, a part that contains the Mo in the Mo alloy powder 2 is diffused in iron-based powder 1 particle and adheres to (diffusion is adhered to) to the surface of iron-based powder 1.
An example of the manufacture method of alloy steel powder for powder metallurgy of the present invention then is described.
In the manufacturing of powdered alloy steel, shown in manufacturing process's example (calcspar) of Fig. 2, at first prepare with the Mo of ormal weight and Mn as alloying component (promptly as prealloy) in advance and the iron-based powder (raw material) that contains (a) with as the Mo material powder (b) that contains the Mo alloy powder.
As iron-based powder (a), preferably, water or gas are sprayed to molten steel and the atomized iron powder that obtains, and wherein, the alloying component that will need contain as prealloy in described molten steel is adjusted to ormal weight.Atomized iron powder is implemented in heating in the reducing atmosphere (for example nitrogen atmosphere) and the processing of reduction C and O usually after atomizing.But iron-based powder of the present invention (a) also can use the iron powder of not implementing this heat treated what is called " spray pattern " (" as atomized ").
In addition, as long as composition is fit to use reduced iron powder, electrolytic iron powder, pulverizing iron powder etc. also no problem no problemly.
As Mo material powder (b), can use metal M o powder or contain the Mo alloy powder, that can use also perhaps that reducible one-tenth contains the Mo alloy powder contains the Mo compound.But, preferably in fact do not contain Mo, Fe metallic element in addition.
Contain the Mo alloy powder, can use pure Mo metal dust or commercially available molybdenum-iron be formed the alloy powder of powder.And, also can use the Fe-Mo alloy that contains the Mo more than the 5 quality % is carried out water atomization or gas atomization and the powder that obtains.
And,, can use Mo oxide, Mo carbide, Mo sulfide, Mo nitride or their complex chemical compound etc. as containing the Mo compound.Consider the easiness of the easiness obtain and reduction reaction and preferred Mo oxide.In addition, contain the Mo compound with powder or by with iron-based powder mix and form that powdered is carried out in processing such as reduction is used.The main component that contains the Mo alloy powder that contains the Mo compound and obtain of reducing is Mo or Fe-Mo.
No matter which kind of situation as the method that makes the Mo material powderization, can be used any means such as pulverizing, atomizing processing.
Then, the ratio with regulation mixes (c) above-mentioned iron-based powder (a) and Mo material powder (b).Mix (c) and can use the arbitrary method (for example Henschel mixer, tapered mixer etc.) that to use.In order to improve the tack of iron-based powder (a) and Mo material powder (b), also can below 0.1 quality %, the scope of (value of the total 100 quality % of iron-based powder (a) and Mo material powder (b) relatively) add the spindle wet goods.Preferably, in order to bring into play the effect of spindle wet goods, preferably add more than the 0.005 quality %.
By in the reducing atmosphere of nitrogen atmosphere, hydrogeneous atmosphere etc., heat-treating (d), can obtain Mo to contain the powdered alloy steel (e) that the diffusion of Mo alloy powder form is adhered to for this mixture.In addition, also can under vacuum, heat-treat (d).Preferably, heat treated temperature is more than 800 ℃, below 1000 ℃.
And, with the iron powder of high C, the O of spray pattern amount during as iron-based powder (a), preferably, by heat treatment (d) and form reducing atmosphere and reduce C and O.And, when using the iron powder of spray pattern as iron-based powder (a), owing to adhere to reduction C and O in the processing in diffusion, the iron-based powder surface becomes activity, thus based on the diffusion that contains Mo alloy (comprising metal M o) attached to also taking place reliably under the low temperature (800～900 ℃), thereby preferred.
In addition, describe below with other compositions for the content of the C, the O that are fit in the powdered alloy steel.
Certainly, when use contains the Mo alloy powder as Mo material powder (b), contain and take place between Mo alloy powder 2 and the iron-based powder 1 to spread to adhere to.
On the other hand, when using Mo oxidate powder etc. to contain the Mo compound, in above-mentioned heat treatment (d), contain the form that the Mo compound is reduced into metal M o as the Mo material powder.Its result, with use as Mo material powder (b) contain the Mo alloy powder situation in the same manner, can obtain adhering to and partly having increased the state of Mo content by diffusion.
Use atomizes to above-mentioned Fe-Mo alloy and during the powder that obtains, can implement final reduction back to this powder and implement heat treatment (d).But, also can with identical main points such as Mo oxidate powder, the Fe-Mo alloy powder of spray pattern is supplied in heat treatment (d).
In addition, contain the Mo alloy powder and compare with using as Mo material powder (b), from the viewpoint of degree of adhering to, the preferred use contains the Mo compound.This is because because the surperficial relative diffusion reaction that contains Mo alloy powder 2 that is reduced in heat treatment step becomes activity, thereby the degree of adhering to of relative iron-based powder 1 is better.
When heat-treating (d) as described above, usually because iron-based powder 1 and contain Mo alloy powder 2 sintering and become curdled appearance, thereby crushing and classification becomes desirable particle diameter, further implements annealing and formation powdered alloy steel 4 as required.
Then the qualification reason for the alloying element amount in the powdered alloy steel 4 describes.
Mo:0.2～1.5 quality the % that contain as prealloy
In powdered alloy steel 4 of the present invention, be included in the Mo content in the iron-based powder 1 as prealloy (promptly in advance as alloying component), the quality of powdered alloy steel 4 is 0.2～1.5 quality % relatively.When the Mo content that contains as prealloy surpassed 1.5 quality %, the effect that hardenability improves did not have big change yet, and the sclerosis owing to powdered alloy steel 4 particles reduces compressibility on the contrary, thereby not preferred.Consider it also is disadvantageous from economic aspect.And the powdered alloy steel 4 that the Mo that contains as prealloy is contained quantity not sufficient 0.2 quality % forms, and carries out sintering then, when carrying out Carburization Treatment and quenching then, in sintered body, separate out ferritic phase easily, its result, sintered body is soft and become intensity, material that fatigue strength is low.
Below the Mn:0.5 quality % that makes in prealloy and contain
The quality that is included in the relative powdered alloy steel 4 of Mn in the iron-based powder 1 as prealloy is below the 0.5 quality %.When surpassing 0.5 quality % as the Mn content of prealloy, the effect that the hardenability that can not obtain matching with Mn content improves, on the contrary, powdered alloy steel 4 sclerosis and compressibility is reduced.And can superfluously consume Mn, cause the rising of manufacturing cost.
In addition, because Mn has some strengthening effects, thereby can contain in above-mentioned scope wittingly, but needn't thereby lower limit be set owing to former on the material.On the other hand, Mn is more as unavoidable impurities contains 0.04 quality % in iron-based powder 1 situation.The processing of removing Mn in order to make Mn be reduced to less than 0.04 quality % needs for a long time, thereby causes the rising of manufacturing cost.Thereby preferred 0.04～0.5 quality % of Mn.
The diffusion adhesion amount of Mo: 0.05～1.0 quality %
Iron-based powder 1 contains Mo and Mn as prealloy, makes to contain the Mo alloy powder and spread to adhere on the surface of its iron-based powder 1 and promptly obtain powdered alloy steel 4.Powdered alloy steel 4 is as the Mo content [Mo] of prealloy
PThe average content [Mo] of (the quality % of the quality of powdered alloy steel 4 relatively) and Mo
T(the quality % of the quality of powdered alloy steel 4 relatively) needs to satisfy following (1) formula:
0.05≤[Mo]
T-[Mo]
P≤ 1.0 (units: quality %) ... (1)
[Mo] in the formula
T-[Mo]
PThe essence implication for diffusion attached to the lip-deep Mo amount of iron-based powder 1 (though exist a little free state contain the Mo alloy powder, ignore at this), below with [Mo]
T-[Mo]
PNote is made the diffusion adhesion amount.
During the diffusion adhesion amount less than 0.05 quality % of Mo, the effect that hardenability improves is less, and the effect that the sintering of powdered alloy steel 4 contact-making surface each other promotes is also less.On the other hand, even the diffusion adhesion amount of Mo surpasses 1.0 quality %, the effect that hardenability improves, sintering promotes is not almost improved, and causes resulting from the rising of the outspent manufacturing cost of Mo.In addition, preferably, the diffusion adhesion amount less than 0.5 quality % of Mo.
And the average grain diameter that contains Mo alloy powder 2 is 20 μ m when following, the fatigue strength of sintered body etc. to improve effect more obvious.On the other hand, according to the viewpoint of the operability in the manufacturing process, be preferably more than the 1 μ m.The average grain diameter that contains Mo alloy powder 2, the laser diffraction and scattering method by foundation JIS standard R1629 (version in 1997) are measured particle diameter and are distributed, and the accumulative perception that adopts volume reference is the value of 50% diameter.
And the Mo degree of adhering to of definition is below 1.5 in following formula (2), is preferably 1.2 when following, fatigue strength etc. to improve effect more obvious.
Wherein, [Mo]
SBe Mo content, represent with the quality % of this fine alloy comminuted steel shot integral body relatively with fine alloy comminuted steel shot (being classified into material below the 45 μ m) by JIS standard Z8801 specified standard sieve screening powdered alloy steel 4.As describing [Mo]
TBe the Mo content (the quality % of the quality of powdered alloy steel 4 relatively) in the powdered alloy steel 4.
And, contain the Mo alloy powder equably attached to iron-based powder in and do not have under the state that contains the Mo alloy powder of free state, Mo degree of adhering to becomes 1.According to rare unbalanced viewpoint, Mo degree of adhering to is preferred more than 0.9, and is further preferred more than 1.0.
Mo degree of adhering to=[Mo]
S/ [Mo]
T(2)
Alloying element beyond above-mentioned, when for example Ni, V, Cu, Cr etc. add in the iron-based powder as prealloy, because compressibility obviously reduces, the density of sintered body reduces and also obvious variation of intensity, fatigue strength, thereby is preferably limited to the content of impurity levels.Particularly, in iron-based powder, preferably, Ni:0.03 quality % is following, V:0.03 quality % is following, Cu:0.03 quality % is following, Cr: less than 0.02 quality % (the quality % of the quality of powdered alloy steel relatively).Further preferably, Ni:0.02 quality % is following, V:0.02 quality % following, Cu:0.02 quality % is following, below the Cr:0.01 quality %.
And, in these alloying elements, except Ni, Cu, do not wish equally to adhere to and be included in the powdered alloy steel by diffusion.Therefore, preferably, in powdered alloy steel, be limited in equally in the above-mentioned compositing range.
For the Ni and/or the Cu that are coupled in the mixed powder, allow that the mode of adhering to diffusion is included in the powdered alloy steel.But, preferred other fit systems according to constrictive viewpoint, thereby in powdered alloy steel, also may be limited to above-mentioned compositing range.
As the impurity that is included in iron-based powder and the powdered alloy steel, can enumerate C: about 0.02 quality % is following, O: about 0.2 quality % is following, N: about 0.004 quality % is following, Si: about 0.03 quality % is following, P: about 0.03 quality % is following, S: about 0.03 quality % is following, Al: about 0.03 quality % following (all being the quality % of relative powdered alloy steel).In addition, original impurity does not need lower limit, but industrial reduction limit (value substantially) is as described below: C:0.001 quality %, O:0.02 quality %, N:0.0001 quality %, Si:0.005 quality %, P:0.001 quality %, S:0.001 quality %, Al:0.001 quality %.
Preferably, the surplus except composition described above is an iron.
As described above, powdered alloy steel 4, owing to the amount that is included in the element in the iron-based powder 1 as prealloy is less, thereby the hardness of powdered alloy steel 4 is suppressed in low level, and can obtain highdensity formed body by the compression molding of powdered alloy steel 4.And owing to the high concentration segregation Mo (promptly being formed with Mo high concentration portion) is arranged on the surface of iron-based powder 1 particle, thereby during the formed body of sintered alloy comminuted steel shot 4, it is single-phase to form α on powdered alloy steel 4 contact-making surface each other.Its result has promoted powdered alloy steel 4 combination each other based on sintering.
As the state of suitable in the present invention Mo high concentration portion, preferably, Mo concentration is the above zones of 2.0 quality %, in the area occupation ratio of relative this powdered alloy steel sectional area, exists more than 1%, below 30%.That is, the zone of Mo concentration more than 2.0 quality %, obviously good for the facilitation effect of the generation of α phase and sintering, and should the zone have 1% when above, on powdered alloy steel contact point each other, exist the frequency of Mo high concentration portion obviously to increase fully.In addition, this zone surpasses at 30% o'clock, and the sintering facilitation effect has saturated trend, from cost and, avoid constrictive unnecessary reduction angle, it is effective setting the upper limit for 30%.Be limited to 20% on further preferred.And this regional Mo concentration also can be 100 quality %.And beyond this zone, Mo is essentially more than the prealloy concentration (minimum 0.2 quality %), less than 2.0 quality %.
Whether satisfy above-mentioned Mo high concentration portion state, particle cross section that can be by analyzing powdered alloy steel with EPMA (diameter of selecting the cross section at average grain diameter ± 10% with interior cross section), measure Mo concentration more than 2.0 quality % the zone and calculate its area by image analysis, thereby can confirm.
And in the present invention, though the average grain diameter of iron-based powder 1 is not limited to specific numerical value, preferably can be in the scope of industrial 30～120 μ m that make with low cost.Wherein, average grain diameter is meant the size distribution of measuring by by the standard screen of JIS standard Z8801, and accumulating weight is distributed as the particle diameter more than 50%.
In the scope of also preferred 30～120 μ m of the average grain diameter of powdered alloy steel 4.
Having cooperated the Ni powder of ormal weight and/or the powder of Cu powder in the powdered alloy steel 4 of above explanation, is mixed powder for powder metallurgy of the present invention.Then, describe for the Ni powder and the Cu powder that cooperate in the powdered alloy steel 4.In addition, the use level (quality %) of following Ni powder and Cu powder is meant the ratio of 100 mass fractions (100 quality %) of relative powdered alloy steel 4.
Ni powder: 0.2～5 quality %
The Ni powder has the sintering reaction activation that makes powdered alloy steel 4, and makes the emptying aperture miniaturization of sintered body and improve the hot strength of sintered body and the effect of fatigue strength.During Ni use level less than 0.2 quality %, can not obtain making the effect of sintering reaction activation.On the other hand, when surpassing 5 quality %, the retained austenite in the sintered body obviously increases, and the intensity of sintered body reduces.Thereby the Ni powder need cooperate in the scope of 0.2～5 quality %.Preferred 0.5～3 quality %.
In addition, as the Ni powder, can use the Ni powder that reduces the Ni oxide and make, the known in the past Ni powder such as carbonyl Ni powder that pass through thermal decomposition method (carbonyl process) manufacturing.Wherein, above-mentioned use level is the value under metal Ni converts.
Cu powder: 0.2～3 quality %
The Cu powder has under the sintering temperature of powdered alloy steel 4 liquid phase of formation and the acceleration of sintering reaction, and makes the emptying aperture nodularization of sintered body and improve the hot strength of sintered body and the effect of fatigue strength.During Cu use level less than 0.2 quality %, the effect of the intensity of the sintered body that can not be improved.On the other hand, when surpassing 3 quality %, sintered body is become fragile.Thereby the Cu powder need cooperate in the scope of 0.2～3 quality %.Preferred 1～2 quality %.In addition, as the Cu powder, can use known in the past Cu powder such as electrolysis Cu powder, atomizing Cu powder.Wherein, above-mentioned use level is the value under metal Cu converts.
Ni powder, Cu powder can perhaps also can all be coupled to both sides in the powdered alloy steel 4 wherein any one is coupled in the powdered alloy steel 4.When only cooperating a kind of in Ni powder or the Cu powder, at the range fit Ni powder of 0.2～5 quality %, perhaps at the range fit Cu powder of 0.2～3 quality %.When cooperating Ni powder and Cu powder both sides, at the range fit Ni powder of 0.2～5 quality %, and at the range fit Cu powder of 0.2～3 quality %.
And, the average grain diameter that makes the Ni powder below 20 μ m, the average grain diameter of Cu powder when 30 μ m are following, the fatigue strength of sintered body etc. to improve effect more obvious.On the other hand, according to the viewpoint of the operability in the manufacturing process, all be preferably more than the 1 μ m.The determination method of average grain diameter can be with to contain Mo alloy powder 2 identical.
In the present invention, also can only Ni powder and/or Cu powder be mixed in the powdered alloy steel.And, also can Ni powder and/or Cu powder be attached on the powdered alloy steel with adhesive (binding agent).Perhaps, also can cooperate Ni powder and/or Cu powder after, implement heat treatment and their diffusions be attached in the powdered alloy steel 4.
When enforcement adhesive attachment or diffusion are adhered to, the segregation of Ni powder, Cu powder can be prevented, the deviation of the characteristic of sintered body can be reduced.But, as mentioned above, because diffusion adheres to and may bring constrictive reduction, thereby adhesive attachment most preferably.
Though adhesive is not limited to specific material, can use
Metallic soap such as zinc stearate, calcium stearate,
Amide-based wax such as ethylenebisstearamide, stearic acid monoamides
In known in the past adhesive.Particularly above-mentioned each adhesive also has lubricating function concurrently and is fit to, but also can use PVA (polyvinyl alcohol), acetate butadiene copolymer, the so not high adhesive of lubricating function of phenolic resin.Wherein, the function when lubricating function is press molding is meant the function of improvement of raising, the withdrawing pattern of the formed body density that is obtained by the powder permutatation.
Though these adhesives can make Ni powder, Cu powder attached on the iron-based powder surface to (comprising eutectic point) more than the fusing point by heating and melting, by adhering to of adhesive being not limited to this method.For example, also can use dissolved adhesive composition in solvent and be coated to iron-based powder and contain on the Mo alloy powder, both are adhered to, make the method for solvent evaporates then.When using above-mentioned adhesive such as metallic soap, preferably containing fusing point is 80～150 ℃ of left and right sides adhesives, and it is above and Ni powder, Cu powder are adhered to be heated to the fusing point of these materials.
In addition, confirmed the Ni that contains as prealloy almost not effect of miniaturization for emptying aperture.Therefore, need add Ni by cooperations such as mixing.
The fiting effect of Ni powder is compared with the fiting effect of Cu powder, cooperate the Ni powder obtain bending fatigue strength etc. to improve effect more obvious.
For above Ni powder, the influence of Cu powder interpolation and the influence of addition manner thereof, infer that its principle is as follows.
Press fatigue strength about face, because the form of stress is mainly compression stress, thereby the densification of sintered body is most important.But, about rotoflector fatigue, tensile stress is arranged, thereby size, the shape of remaining emptying aperture exerts an influence as the factor that can not ignore in the sintered body owing to except compression stress, also act on.Therefore, think the cooperation of Ni powder, Cu powder, owing to improve the effect of the form of emptying aperture, play great role for the improvement of rotoflector fatigue strength etc.
Wherein, think that improving effect according to the emptying aperture form of Ni, Cu showed in the sintering later stage that fully forms emptying aperture.Therefore, think the combination of adhering to prealloy and diffusion to add Mo and promote the miniaturization of emptying aperture, and the mode to the formal diffusion of emptying aperture periphery in the sintering later stage with simple mixing, adhesive attachment etc. cooperates in the combination of Ni, Cu, shows tangible composite effect.
Then, the condition of using mixed powder for powder metallurgy of the present invention and being fit to when making sintered body is described.
Preferably, before carrying out press molding, use the carbonaceous powders such as graphite powder of (values of mixed powder 100 mass fractions relatively) about powder 0.1～1.2 mass fraction as alloy for mixed powder.And, also can add known machinability and improve with powder (MnS etc.).In addition, further preferably, carbonaceous powder, machinability are improved with powder also use adhesive and attached on the powdered alloy steel.
And, before press molding, lubricant that can the mixed powder powder.And, also can on metal die, apply or adhere to lubricant.The whichever purpose, as lubricant, be suitable for following be used to reduce when being shaped powder each other or the lubricant of the friction between powder and the metal die:
Metallic soap (for example zinc stearate, lithium stearate, calcium stearate etc.),
Fatty acid amide known lubricants such as (for example stearic amide, ethylenebisstearamide, erucyl amides etc.).
Preferably, the lubricant that is mixed is (value of mixed powder 100 mass fractions relatively) about 0.1～1.2 parts by weight.
As mentioned above, also can when hybrid lubricant, heat, with lubricant as adhesive as and make Ni powder, Cu powder attached on the powdered alloy steel.
Preferably, with the pressure about 400～1000MPa, implement press molding in normal temperature (about 20 ℃)～about 160 ℃ temperature.For manufacturing process, known method all is fit to.For example, making the iron-based powder mixed powder is room temperature, and metal die is heated to 50～70 ℃ method, because the processing of powder easily and can further improve the density (press-powder volume density) of iron-based powder formed body, thereby is fit to.And, can also use powder, metal die to be heated to 120～130 ℃ so-called thermo shaping method simultaneously.
Preferably, about 1100～1300 ℃, implement sintering.According to viewpoint economically, preferably, with cheapness and mass producible meshbeltfurnace at the possible sintering that carries out below 1160 ℃.Further preferred below 1140 ℃.Preferred especially about 10～60 minutes of sintering time.The stove that also can use other is push-plate formula sintering furnace etc. for example.
For resulting sintered body, can implement intensive treatment such as carburizing and quenching (CQT), bright quenching (BQT), high-frequency quenching, nicarbing heat treatment as required.Implement to quench when waiting, also can further implement temper.Each intensive treatment condition is set according to conventional methods and is got final product.In addition, when not implementing intensive treatment, compare with existing sintered body (not implementing intensive treatment), bending fatigue strength etc. improve.
And the size of the emptying aperture of sintered body also is subjected to the influence of molding condition, sintering condition.When for example having cooperated the Ni powder, with density as pressed 7.1～7.4Mg/m
3Be shaped, by 1100～1160 ℃, 10～60 minutes sintering, the average emptying aperture diameter of sintered body became about 5～20 μ m, at density as pressed 7.4Mg/m
3More than, become in the sintering more than 1130 ℃, more than 20 minutes below the 10 μ m.
In addition, viewpoint according to hot strength and fatigue strength, preferably, adjust amount, the intensive treatment bar of the carbonaceous powder that mixes, the composition that makes resulting sintered body is C:0.6～1.2 quality %, O:0.02～0.15 quality %, N:0.001～0.7 quality %.
Embodiment
The present invention is described by the following examples in further detail, and mixed powder for powder metallurgy of the present invention and uses thereof all is not limited to following example.
Embodiment 1
The iron-based powder (average grain diameter 70～90 μ m) of spraying and forming spray pattern for the molten steel of Mo that comprises ormal weight and Mn by water atomization.On this iron-based powder, add the MoO of average grain diameter 1～3 μ m with the ratio of regulation
3Powder mixed 15 minutes in V-Mixer as the Mo material powder.
In the nitrogen atmosphere of 30 ℃ of dew points, heat-treat (keeping 875 ℃ of temperature, 1 hour retention time), with MoO for this mixed powder
3Powder reduction becomes the Mo metal dust, and diffusion is attached on the surface of iron-based powder and the alloying comminuted steel shot.And the average grain diameter of whichever powdered alloy steel is all in the scope of 70～90 μ m.Cooperating average grain diameter on this powdered alloy steel is the Ni powder (carbonyl Ni powder) of 4 μ m and the Cu powder (electrolysis Cu powder) that average grain diameter is 20 μ m, and mixes 15 minutes in V-Mixer, forms mixed powder for powder metallurgy.The composition of the mixed powder for powder metallurgy that obtains like this is illustrated in table 1.Surplus in the table beyond the record is essentially iron and impurity.
Table 1
| Specimen coding | Mixed powder for powder metallurgy | Remarks | ||||
| Powdered alloy steel | The Ni powder *(quality %) | The Cu powder *(quality %) | ||||
| Iron-based powder | Mo spreads adhesion amount (quality %) | |||||
| Mn prealloy (quality %) | Mo prealloy (quality %) | |||||
| 1 | 0.21 | 0.62 | 0.0 | 1.0 | - | Comparative example |
| 2 | 0.21 | 0.62 | 0.2 | 1.0 | - | Example |
| 3 | 0.21 | 0.62 | 0.6 | 1.0 | - | |
| 4 | 0.21 | 0.62 | 0.8 | 1.0 | - | |
| 5 | 0.21 | 0.62 | 1.2 | 1.0 | - | Comparative example |
| 6 | 0.19 | 0.12 | 0.4 | 0.5 | 2.0 | |
| 7 | 0.21 | 0.62 | 0.4 | 0.5 | 2.0 | Example |
| 8 | 0.21 | 1.03 | 0.4 | 0.5 | 2.0 | |
| 9 | 0.20 | 1.45 | 0.4 | 0.5 | 2.0 | |
| 10 | 0.19 | 1.79 | 0.4 | 0.5 | 2.0 | Comparative example |
| 11 | 0.56 | 0.59 | 0.4 | 0.5 | 2.0 | |
| 12 | 0.20 | 0.81 | 0.2 | 0.1 | - | |
| 13 | 0.20 | 0.81 | 0.2 | 0.5 | - | Example |
| 14 | 0.20 | 0.81 | 0.2 | 1.0 | - | |
| 15 | 0.20 | 0.81 | 0.2 | 4.0 | - | |
| 16 | 0.21 | 0.62 | 0.6 | - | 0.1 | Comparative example |
| 17 | 0.21 | 0.62 | 0.6 | - | 0.5 | Example |
| 18 | 0.21 | 0.62 | 0.6 | - | 1.0 | |
| 19 | 0.21 | 0.62 | 0.6 | - | 2.0 | |
| 20 | 0.21 | 0.62 | 0.6 | - | 4.0 | Comparative example |
| 21 | 0.10 | 0.60 | 0.2 | 1.0 | - | Example |
| 22 | 0.40 | 0.60 | 0.2 | 1.0 | - | |
| 23 | 0.20 | 0.40 | 0.2 | 1.0 | - | |
| 24 | 0.21 | 0.62 | 0.1 | 1.0 | - | |
| 25 | 0.21 | 0.62 | 0.4 | 1.0 | - | |
*: the situation that "-" expression cooperates
2～No. 4 samples in the table 1 and 13～No. 15 samples are the examples that Mo prealloy amount, Mn prealloy amount, Mo diffusion adhesion amount, Ni powder use level satisfy scope of the present invention.No. 1 sample, No. 5 samples are examples that Mo diffusion adhesion amount departs from the scope of the present invention.
7～No. 9 samples are the examples that Mo prealloy amount, Mn prealloy amount, Mo diffusion adhesion amount, Ni powder use level, Cu powder use level satisfy scope of the present invention.No. 6 samples, No. 10 samples are examples that Mo prealloy amount departs from the scope of the present invention, and No. 11 samples are examples that Mn prealloy amount departs from the scope of the present invention.
No. 12 samples are examples that Ni powder use level departs from the scope of the present invention.
17～No. 19 samples are the examples that Mo prealloy amount, Mn prealloy amount, Mo diffusion adhesion amount, Cu powder use level satisfy scope of the present invention.No. 16 samples, No. 20 samples are examples that Cu powder use level departs from the scope of the present invention.
In these mixed powder for powder metallurgy 100 mass fractions, add the graphite of 0.3 mass fraction as alloying with powder, add the lithium stearate of 0.8 mass fraction as lubricant, and in V-Mixer, mixed 15 minutes.Then, mixed powder for powder metallurgy is heated to 130 ℃, and is filled into metal die (temperature: 130 ℃) and carries out press molding (pressure: 686MPa).
For this formed body, at RX atmosphere (N
2-32 volume %H
2-24 volume %CO-0.3 volume %CO
2) in implement sintering (1300 ℃ of sintering temperatures, sintering time 20 minutes) and form sintered body.After in resulting sintered body, carrying out gas carburizing (keep temperature 870 ℃, 60 minutes retention times) with carbon potential 0.8 quality %, quench (60 ℃ of hardening heats, oil hardening) and tempering (200 ℃ of temperatures, tempering time 60 minutes).Wherein, carbon potential is the index of the carburizing ability of expression atmosphere that steel is heated, and under this temperature, the concentration of carbon on the surface of the steel when reaching balance with this gas atmosphere is represented.
Density, hot strength, the rotoflector fatigue strength of this sintered body have been measured.Its result is as shown in table 2.Wherein, measure density with JIS standard Z2501 as benchmark.Choose from sintered body parallel portion diameter 5mm, length 15mm small-sized round bar sample and carry out stretching experiment and measure hot strength in room temperature.The diameter of choosing parallel portion is that 8mm, length are the level and smooth round bar sample of 15.4mm, and uses little wild formula rotary bending tester, by 10
7The inferior load of not destroying is calculated rotoflector fatigue strength.
Table 2
| Specimen coding | Sintered body | Remarks | ||
| Density (Mg/m 3) | Hot strength (MPa) | Rotoflector fatigue strength (MPa) | ||
| 1 | 7.30 | 1200 | 310 | Comparative example |
| 2 | 7.32 | 1450 | 430 | Example |
| 3 | 7.33 | 1510 | 450 | |
| 4 | 7.34 | 1440 | 430 | |
| 5 | 7.34 | 1210 | 320 | Comparative example |
| 6 | 7.29 | 1270 | 340 | |
| 7 | 7.29 | 1390 | 390 | Example |
| 8 | 7.28 | 1350 | 380 | |
| 9 | 7.26 | 1320 | 370 | |
| 10 | 7.19 | 1190 | 300 | Comparative example |
| 11 | 7.16 | 1 120 | 280 | |
| 12 | 7.29 | 1250 | 320 | |
| 13 | 7.30 | 1340 | 430 | Example |
| 14 | 7.31 | 1480 | 450 | |
| 15 | 7.32 | 1490 | 440 | |
| 16 | 7.31 | 1 170 | 310 | Comparative example |
| 17 | 7.32 | 1310 | 360 | Example |
| 18 | 7.31 | 1360 | 390 | |
| 19 | 7.30 | 1350 | 380 | |
| 20 | 7.28 | 1 100 | 280 | Comparative example |
| 21 | 7.34 | 1470 | 460 | Example |
| 22 | 7.24 | 1340 | 360 | |
| 23 | 7.35 | 1450 | 440 | |
| 24 | 7.31 | 1420 | 410 | |
| 25 | 7.32 | 1460 | 440 | |
As known from Table 2, when example (2～No. 4 samples) in 1～No. 5 sample of comparison and comparative example (No. 1, No. 5 samples), though do not find the difference of density, example one side's hot strength and rotoflector excellent in fatigue strength.
When example (7～No. 9 samples) in 6～No. 11 samples of comparison and comparative example (No. 6, No. 10, No. 11 samples), density, hot strength, rotoflector fatigue strength all are that a side of example is good.
When example (13～No. 15 samples) in 12～No. 15 samples of comparison and comparative example (No. 12 samples), though do not find the difference of density, hot strength and rotoflector fatigue strength are that a side of example is good.
When example (No. 17, No. 19 samples) in 16～No. 20 samples of comparison and comparative example (No. 16, No. 20 samples), though do not find the difference of density, hot strength and rotoflector fatigue strength are that a side of example is good.
Embodiment 2
With method similarly to Example 1, Mo, Mn that manufacturing makes ormal weight make Mo (Mo metal powder, Fe-10 quality %Mo, the Fe-50 quality %Mo) diffusion of ormal weight be attached to lip-deep powdered alloy steel as prealloy.In this powdered alloy steel, add Ni powder, the 0.3 quality % of the average grain diameter 4 μ m of ormal weight graphite powder, hold concurrently adhesive and add the ethylenebisstearamide of 0.6 mass fraction as lubricant, be heated to 160 ℃ and mixed 10 minutes, make the Ni powder attached to (No. 26, No. 29, No. 30 samples) on the powdered alloy steel surface.Wherein, mix interpolation Ni powder after heating mixed processing, in addition, form mixed powder by same processing for No. 31 interpolation adhesives.And,, strengthened sintering (1250 ℃ of-60 minutes, N for No. 32 and as No. 33 of the comparative example of forming
2-10 volume %H
2In the atmosphere).
And, also made and made the lip-deep powdered alloy steel (No. 27 sample) of Ni powder diffusion attached to iron-based powder.And, as a comparison, also made Mo, Mn with ormal weight with Ni as prealloy, the powdered alloy steel (No. 28 samples) of the Mo of ormal weight is adhered in diffusion from the teeth outwards.In these powdered alloy steels, add the graphite powder of 0.3 quality %, hold concurrently adhesive and add the ethylenebisstearamide of 0.6 mass fraction, and be heated to 160 ℃ and carried out mixing in 10 minutes as lubricant.
For these mixed powders, shaping, sintering, carburizing have been carried out by method similarly to Example 1.Then, obtain density, hot strength, rotoflector fatigue strength, the average emptying aperture diameter of these sintered bodies.Its result is shown in table 3, table 4.Wherein, carry out mirror ultrafinish for the cross section of sintered body, for visual field 50cm
2The light microscope photographs carry out image analysis, and obtain average emptying aperture diameter with the method for approximate circle diameter.
Table 3
| Specimen coding | Powdered alloy steel | Remarks | |||||
| Iron-based powder | Diffusion is adhered to | Add | |||||
| Mn prealloy amount (quality %) | Mo prealloy amount (quality %) | Ni prealloy amount (quality %) | Mo spreads adhesion amount (quality %) | Ni spreads adhesion amount *4(quality %) | The Ni powder *4(quality %) | ||
| 26 | 0.19 | 0.60 | - | 0.15 | - | 1 | Example |
| 27 | 0.19 | 0.60 | - | 0.15 | 1 | - | |
| 28 | 0.19 | 0.60 | 1.00 | 0.15 | - | - | Comparative example |
| 29 *1 | 0.19 | 0.60 | - | 0.15 *3 | - | 1 | Example |
| 30 *2 | 0.19 | 0.60 | - | 0.15 *3 | - | 1 | |
| 31 | 0.19 | 0.60 | - | 0.15 | - | 1 *5 | |
| 32 *6 | 0.19 | 0.60 | - | 0.15 | - | 1 | |
| 33 *6 | 0.19 | 0.60 | - | 0.15 | - | - | Comparative example |
*1: use Fe-10 quality %Mo powder as the Mo source
*2: use Fe-50 quality %Mo powder as the Mo source
*3: be converted into metal M o
*4: the situation that "-" expression cooperates
*5: do not use adhesive
*6: sintering condition be 1250 ℃-60 minutes
Table 4
| Specimen coding | Sintered density (Mg/m 3) | Hot strength (MPa) | Rotoflector fatigue strength (MPa) | Mean void diameter (μ m) | Remarks |
| 26 | 7.35 | 1460 | 490 | 10.1 | Example |
| 27 | 7.32 | 1410 | 450 | 10.8 | |
| 28 | 7.25 | 1220 | 310 | 13.6 | Comparative example |
| 29 | 7.35 | 1450 | 480 | 10.5 | Example |
| 30 | 7.37 | 1455 | 487 | 10.3 | |
| 31 | 7.34 | 1440 | 470 | 10.2 | |
| 32 | 7.43 | 1510 | 500 | 8.0 | |
| 33 | 7.35 | 1280 | 350 | 11.4 | Comparative example |
The example of No. 26, No. 27, No. 29, No. 30 samples is compared with the comparative example of No. 28 samples, and average emptying aperture diameter diminishes, and hot strength and rotoflector fatigue strength are that a side of example is good.And, making the Ni powder adhere to (No. 27 samples) with diffusion with adhesive and compare attached to the side on the powdered alloy steel (No. 26, No. 29, No. 30 samples), the hole diameter diminishes, and has also improved rotoflector fatigue strength.
Embodiment 3
With similarly to Example 1 method with Mo, the Mn of ormal weight as the iron-based powder of prealloy in the quantitative Mo material powder (MoO of hybrid regulatory
3Powder).For this mixed-powder, in the nitrogen atmosphere of 30 ℃ of dew points, heat-treat with the maintenance temperature (900～1050 ℃) different with embodiment 1, made the powdered alloy steel shown in 34～No. 36 of table 5.In addition, 1～of embodiment 1 No. 5 powdered alloy steel is illustrated in the table 5 simultaneously.
Measured the area occupation ratio in the zone of Mo concentration more than 2.0 quality % by following method.After imbedding powdered alloy steel in the resin, grind, choose 10 particle cross sections (diameter of section average grain diameter ± 10% with interior part) and analyze by EPMA, measure the zone of Mo concentration more than 2.0 quality %, calculate its area by image analysis.The value (10) that obtains from each cross section is averaged and as the area occupation ratio in the zone of Mo concentration more than 2.0 quality %.
For each powdered alloy steel of table 5, mix the Ni powder of 1.0 quality %, after the method by similarly to Example 1 obtains sintered body, measured density, hot strength and rotoflector fatigue strength.The result is illustrated in table 6.
Table 5
| Specimen coding | Powdered alloy steel | Appendix | ||||
| Iron-based powder | Mo spreads adhesion amount (quality %) | The diffusion adhere to temperature (℃) | The area occupation ratio (%) in the zone that Mo concentration 2.0 quality % are above | |||
| Mn prealloy (quality %) | Mo prealloy (quality %) | |||||
| 1 | 0.21 | 0.62 | 0.0 | 875 | 0 | Comparative example |
| 2 | 0.21 | 0.62 | 0.2 | 875 | 3 | Example |
| 3 | 0.21 | 0.62 | 0.6 | 875 | 10 | |
| 4 | 0.21 | 0.62 | 0.8 | 875 | 16 | |
| 5 | 0.21 | 0.62 | 1.2 | 875 | 32 | Comparative example |
| 34 | 0.19 | 0.12 | 0.4 | 900 | 4.0 | Example |
| 35 | 0.21 | 0.62 | 0.4 | 950 | 2.0 | |
| 36 | 0.21 | 1.03 | 0.4 | 1000 | 1.0 | |
Table 6
| Specimen coding | Sintered body | Appendix | ||
| Density (Mg/m 3) | Hot strength (MPa) | Rotoflector fatigue strength (MPa) | ||
| 1 | 7.30 | 1200 | 310 | Comparative example |
| 2 | 7.32 | 1450 | 430 | Example |
| 3 | 7.33 | 1510 | 450 | |
| 4 | 7.34 | 1440 | 430 | |
| 5 | 7.34 | 1210 | 320 | Comparative example |
| 34 | 7.31 | 1450 | 480 | Example |
| 35 | 7.29 | 1400 | 450 | |
| 36 | 7.27 | 1380 | 430 | |
From table 5, table 6 as can be known, the area occupation ratio in the zone of Mo concentration more than 2.0 quality % is compared hot strength and rotoflector excellent in fatigue strength in the example (2～No. 4,34～No. 36) of 1～30% scope with comparative example (No. 1, No. 5).
Utilize possibility on the industry
Use mixed powder for powder metallurgy of the present invention, do not use special sintering circuit, also can produce the sintered body with good hot strength and bending fatigue strength and densification.
Claims (3)
1. mixed powder for powder metallurgy, in the powdered alloy steel that comprises the Mo:0.05～1.0 quality % that contain below the Mn:0.5 quality % as prealloy and adhere to powder type diffusion on the iron-based powder of Mo:0.2～1.5 quality % and the surface, add the Ni powder at least: 0.2～5 quality % and Cu powder: any one among 0.2～3 quality % and forming at this iron-based powder.
2. mixed powder for powder metallurgy, in powdered alloy steel, at least add the Ni powder: 0.2～5 quality % and Cu powder: any one among 0.2～3 quality % and forming, wherein, Mo concentration be the above zone of 2.0 quality % on the surface of described powdered alloy steel, have more than 1% of area of section, below 30%, and, the surplus of this powdered alloy steel be Mo concentration more than 0.2 quality %, the zone of less than 2.0 quality %.
3. mixed powder for powder metallurgy according to claim 1 and 2 wherein, makes at least a by forming on the surface of binding agent attached to described powdered alloy steel in described Ni powder and the Cu powder.
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| CN110267754B (en) * | 2017-02-02 | 2021-10-29 | 杰富意钢铁株式会社 | Mixed powder for powder metallurgy, sintered body, and method for producing sintered body |
| CN112458372A (en) * | 2019-09-06 | 2021-03-09 | 现代自动车株式会社 | Iron-based prealloyed powder, iron-based diffusion-bonded powder, and iron-based alloy powder for powder metallurgy using same |
| CN112458372B (en) * | 2019-09-06 | 2023-10-13 | 现代自动车株式会社 | Iron-based prealloyed powder, iron-based diffusion bonded powder, and iron-based alloy powder for powder metallurgy using same |
| CN111570798A (en) * | 2020-06-28 | 2020-08-25 | 南通旺鑫新材料有限公司 | Powder metallurgy solution infiltration bonding method |
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