CN102534349A - Alloy steel powder for powder metallurgy, iron-based sintering material and manufacturing method thereof - Google Patents
Alloy steel powder for powder metallurgy, iron-based sintering material and manufacturing method thereof Download PDFInfo
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Abstract
The present invention provides an alloy steel powder for powder metallurgy, which is provided with high strength and high toughness. The invention also provides an iron-based sintering material and a manufacturing method thereof. The alloy steel powder for powder metallurgy is formed through diffusing and adhering the powder which comprises 0.05-1.5wt% of Mo on the surface of the steel powder which is alloyed with 0.02-0.4% of Nb.
Description
Technical field
The present invention relates to be fit to be provided in the alloy steel powder for powder metallurgy of PM technique, particularly using said Powdered Alloy Steel to make intensity and the flexible Powdered Alloy Steel that is used to realize improving said agglomerated material under the situation of agglomerated material.
In addition, the present invention relates to use the intensity of above-mentioned alloy steel powder for powder metallurgy manufacturing and the agglomerated material and the method for manufacture thereof of good-toughness.
Background technology
PM technique can be made the parts of complicated shape with the shape very close with article shape (so-called nearly end form) and with high size precision, therefore, can greatly reduce the cutting cost.Therefore, sintered metal product is used as various machineries, parts in many-side.
And recently, for miniaturized, the lightweight that realizes parts, strong request improves the intensity of sintered metal product.Particularly the high strength to iron-based powder goods (iron base sintered body) requires strong.
The iron-based powder for powder metallurgy molding is generally made through following operation: in iron-based powder, sneak into alloys such as copper powder, Graphite Powder 99 and process the iron-based powder powder mix with lubricants such as powder and Triple Pressed Stearic Acid, lithium stearates, fill it into then and carry out press molding in the mould.According to composition, can iron-based powder be categorized as iron powder (for example straight iron powder etc.), Powdered Alloy Steel etc.In addition, carry out the branch time-like according to method of manufacture, can be categorized as atomized iron powder, reduced iron powder etc., in these classification, iron powder uses the broad sense that comprises Powdered Alloy Steel.
The density of the molding that is obtained by common powder metallurgy operation is generally about 6.6Mg/m
3～about 7.1Mg/m
3Then, these iron-based powder moldinies are implemented sintering processes and processed sintered compact, and then implement pressure-sizing processing, cut as required, thereby process sintered metal product.And, under the situation of the higher intensity of needs, also behind sintering, implement carburizing thermal treatment, bright heat treatment sometimes.
In the stage of raw material powder, as the powder that has added alloying element, known following powder etc.:
(1) in straight iron powder, mixed the powder mix of each alloying element powder;
(2) fully alloying the prealloy comminuted steel shot of each element;
(3) make each alloying element powder adhere to the part diffusion alloy comminuted steel shot of diffusion on the surface portion ground of straight iron powder, prealloy comminuted steel shot.
(1) the powder mix that in straight iron powder, has mixed each alloying element powder has the advantage that can guarantee with the equal high-compressibility of straight iron powder.But but there is following problem: when carrying out sintering, if not with the CO in sintering atmosphere, the carburizing atmosphere
2Concentration and dew point are strict controlled in lower level, then as than the Mn of the more active metal of Fe, Cr, V, Si, Nb, Ti etc. oxidation can taking place, thereby can not realize low oxygen contentization; And each alloying element is also insufficient diffusion in Fe, forms uneven tissue, thereby can not reach matrix strengthening.
Therefore, the powder mix that in straight iron powder, has mixed each alloying element powder of (1) can not be tackled the requirement of high strength in recent years, so that is in the state that is not used.
Relative therewith; (2) complete alloying the prealloy comminuted steel shot of each element have following advantage: though owing to make through molten steel is atomized; Thereby can produce the solution hardening effect that causes by oxidation in the atomizing operation of molten steel and complete alloying; But, limit through kind and amount alloying elements such as Mn, Cr, V, Si, Nb, Ti, can guarantee low oxygen contentization and with the equal high-compressibility of straight iron powder.In addition, there is the possibility that causes matrix strengthening by complete alloying, therefore developing with the prealloy comminuted steel shot as HS.
In addition; (3) part diffusion alloy comminuted steel shot; Metal-powder through in straight iron powder, prealloy comminuted steel shot, mixing each element and under the atmosphere of non-oxidizable or irreducibility, heat so that each metal-powder on the surface portion ground of straight iron powder, prealloy comminuted steel shot diffusion bond make; Therefore, it can make up the advantage of prealloy comminuted steel shot of iron base powder mixture and (2) of (1).Therefore; Can guarantee low oxygen contentization and with the equal high-compressibility of straight iron powder; And exist by forming the possibility that causes matrix strengthening by the complete alloy phase complex tissue that enrichment constitutes mutually with part, therefore, as HS with partly spreading the prealloy comminuted steel shot and developing.
Basic alloys composition as above-mentioned prealloy comminuted steel shot and part diffusion alloy comminuted steel shot in most cases uses Mo.Its reason and Mo can be identical as the reason of the strengthening element of ferrous materials.Promptly; This is because Mo not only suppresses ferritic generation, makes bainite structureization in ferrous materials, thereby makes parent phase (matrix) phase transformation strengthening; And in parent phase and carbide, distribute and make the parent phase solution strengthening, and then form fine carbide and make the parent phase precipitation strength.In addition, owing to be the good non-grain boundary oxidation element of gas cementation property, therefore also has the effect that carburizing is strengthened.
In addition, make agglomerated material reinforcement aspect, can also add carbide such as V, Nb, Ti and form the strong element of ability from precipitation strength through carbide.
For example, disclose a kind of alloy steel powder for powder metallurgy in the patent documentation 1, it is characterized in that, contained Mo:0.1～6.0%, V:0.05～2.0% and below the Nb:0.10%, and Mo below 4% has partly been spread adhere to through pre-alloyed.This Powdered Alloy Steel guaranteed the powder stage low oxygen contentization and with the equal high-compressibility of iron powder, and realized the low oxygen contentization and the matrix strengthening of agglomerated material or carburizing and quenching material.
In addition; A kind of high-strength sintered body and function Powdered Alloy Steel is disclosed in the patent documentation 2; It is characterized in that, in weight ratio, contain below Cr:0.5～2%, Mn:0.08%, Mo:0.1～0.6%, V:0.05～0.5%; Also contain a kind or 2 kinds in Nb:0.01～0.08%, Ti:0.01～0.08%, and 0.05～3.5% Mo diffusion is adhered to.Should be technological; Can access the Powdered Alloy Steel that compressibility is good, can be controlled to be suitable hardening capacity; And; Through the speed of cooling after using this comminuted steel shot and controlling sintering, can make the fine pearlitic structure of formation in the sintered compact and do not form thick upper bainite tissue, thereby under sintering state, just can access HS.
Patent documentation 1: japanese kokai publication hei 8-49047 communique
Patent documentation 2: japanese kokai publication hei 7-331395 communique
But the inventor's research shows, has used the agglomerated material of any one Powdered Alloy Steel in above-mentioned patent documentation 1 and the patent documentation 2 all to be difficult to have concurrently intensity and toughness.
Summary of the invention
The objective of the invention is to, overcome above-mentioned prior art problems, proposition can have intensity and flexible alloy steel powder for powder metallurgy concurrently.
In addition, the present invention also aims to, provide the agglomerated material that uses intensity that above-mentioned alloy steel powder for powder metallurgy makes and good-toughness, with and favourable method of manufacture.
The inventor has carried out various researchs, the opinion that the result obtains being described below to the alloying constituent and the addition means thereof of iron-based powder in order to achieve the above object repeatedly.
Carbide forming element such as pre-alloyed Nb and iron-based powder that the Mo diffusion is adhered to mix with carbon dust and when processing molding and carrying out sintering, Alloy Elements Mo is in the interparticle sintering neck formation of iron-based powder high density in iron powder.Therefore, in the sintering neck, have carbide forming element and C such as Mo and Nb, and the carbide that contains Mo and Nb etc. is separated out, is disperseed.
Owing to have a large amount of pores in the sintering neck, so the intensity of this part has the tendency of reduction, but when the carbide of above-mentioned that kind when pore is separated out on every side, the sintering neck is reinforced.
On the other hand, owing to do not contain Mo in the matrix part, so it compares with the sintering neck, carbide is difficult to generate, and therefore becomes the tissue of H.T..
The present invention is based on above-mentioned opinion and accomplishes.
That is, main points of the present invention are constructed as follows said.
1. alloy steel powder for powder metallurgy, it is that the Mo powder that contains of 0.05～1.5 quality % adheres in the comminuted steel shot surface diffusion of the Nb of pre-alloyed 0.02～0.4 quality % and forms through making the Mo amount.
2. alloy steel powder for powder metallurgy, it is that at least any one the comminuted steel shot surface diffusion of Mo powder in the Ti of the V of the Nb of pre-alloyed 0.02～0.4 quality % and pre-alloyed 0.01～0.4 quality % and 0.01～0.4 quality % that contain of 0.05～1.5 quality % adhered to and formed through making the Mo amount.
3. iron based material through above-mentioned 1 or 2 described alloy steel powder for powder metallurgy press-powders being shaped, carrying out sintering then and obtain, around the pore of said agglomerated material, is separated out the carbide that contains Nb and Mo at least.
4. as above-mentioned 3 described iron based materials, wherein, the said carbide that contains Nb and Mo at least for (Nb, Mo) C, (Nb, V, Mo) C, (Nb, Ti, Mo) C reach (Nb, Ti, V, Mo) among the C at least any one.
5. the method for manufacture of an iron based material; It is characterized in that; Above-mentioned 1 or 2 described alloy steel powder for powder metallurgy are mixed with the carbon dust of 0.1～1.0 quality %; Under the pressure of 400～1000MPa, carry out press-powder then and be shaped, under 1100～1300 ℃ temperature, carry out sintering then, make the pore of the agglomerated material of gained separate out the carbide that contains Nb and Mo at least on every side.
6. as the method for manufacture of above-mentioned 5 described iron based materials, wherein, the said carbide that contains Nb and Mo at least for (Nb, Mo) C, (Nb, V, Mo) C, (Nb, Ti, Mo) C reach (Nb, Ti, V, Mo) among the C at least any one.
The invention effect
According to the present invention, through use Nb pre-alloyed, or also pre-alloyed V and/or Ti and only make Mo spread the alloy steel powder for powder metallurgy that adheres to, can access the agglomerated material that has HS and H.T. concurrently.
Description of drawings
Fig. 1 is the mode chart of the sintering structure that comprises the sintering neck of the sintered compact that obtained by the present invention of expression.
Label declaration
1 iron-based powder
2 sintering necks
Embodiment
Below, the present invention is specified.
Alloy steel powder for powder metallurgy of the present invention, make contain the Mo powder pre-alloyed Nb, or the comminuted steel shot surface diffusion of also pre-alloyed V and/or Ti adhere to and obtain.
Mix with carbon dust through the iron-based powder that makes the invention described above and to process molding and to carry out sintering, Alloy Elements Mo forms high density at the interparticle sintering neck of iron-based powder.Therefore, in the sintering neck, have Mo and Nb, V, Ti and C, the carbide that contains Mo and Nb, V, Ti etc. is separated out, is disperseed.
Owing to have a large amount of pores in the sintering neck, so the intensity of this part has the tendency of reduction, but when the carbide of above-mentioned that kind when pore is separated out on every side, the sintering neck is reinforced.
On the other hand, owing to do not contain Mo in the matrix part, so it compares with the sintering neck, carbide is difficult to generate, and therefore becomes the tissue of H.T..
As stated, think, can realize HS and H.T. simultaneously through the generation zone of control carbide.
Below, the reason with the pre-alloyed Nb of aforementioned compositing range, V, Ti among the present invention is described.In addition, " % " shown in below is with respect to the overall ratio (quality %) of alloy steel powder for powder metallurgy of the present invention (contain the diffusion of Mo powder and adhere to the back).
Nb：0.02～0.4％
Nb plays very effective function through in matrix, separating out with the carbide form to the raising of intensity.But, when content less than 0.02% the time, the growing amount of carbide becomes insufficient; Can't expect the sufficient high strength of sintered compact, on the other hand, when greater than 0.4% the time; Thickization of carbide, thereby the reduction of intensity raising effect, and owing to the sclerosis of Powdered Alloy Steel particle causes compressibility to reduce; Moreover, also unfavorable from the viewpoint of economy.More preferably 0.05～0.3%.
In V:0.01～0.4% and Ti:0.01～0.4% any one or two kinds
V and Ti be only second to Nb as the useful element of carbide forming element, therefore these elements and Nb are compound to be contained through making, and can further help the raising of intensity.But wherein the interpolation of any one element is less than prescribing a time limit under-ageing down; On the other hand, last carbide still can thickization in limited time when add surpassing, thereby cause intensity to improve that effect reduces, compressibility reduces, and therefore, V, each comfortable above-mentioned scope of Ti contained.More preferably each is comfortable below 0.3%.
In addition, the total amount of Nb, V and Ti is in 0.09～0.18% scope the time, can access to possess good especially intensity and flexible agglomerated material.
Then, the method for manufacture to alloy steel powder for powder metallurgy of the present invention describes.
At first, prepare the containing of predetermined amount as the iron-based powder (as the iron-based powder of raw material) of the alloying element of prealloy composition (that is, as prealloy) and as the Mo raw material powder that contains the raw material of Mo powder.
As iron-based powder, preferred so-called atomized iron powder.Atomized iron powder is meant the iron-based powder of the molten steel of having adjusted alloying constituent according to purpose being sprayed and obtaining through water or gas.For atomized iron powder, common, the heating in reducing atmosphere (for example hydrogen atmosphere) of atomizing back, C in the enforcement minimizing iron powder and the processing of O thus.But,, also can use the iron powder of not implementing this heat treated, so-called " atomizing state " as the iron-based powder of raw material of the present invention.
As the Mo raw material powder, can use as target contain Mo powder itself, perhaps also can use can reductive Mo compound as containing the Mo powder.
Here, as containing the Mo powder, be fit to use pure metal powder and the Mo powdered alloys such as oxidation Mo powder or FeMo (molybdenum-iron) powder of Mo.In addition, as the compound of Mo, preferred Mo carbide, Mo sulfide, Mo nitride etc.
Then, above-mentioned iron-based powder and Mo raw material powder are mixed according to predetermined ratio.About blending means, there is not special limitation, for example can use Henschel mixer, cone mixer etc.
Then, this mixture is at high temperature kept, with the contact surface of Mo raw material powder Mo is spread in iron and engage, thus, obtain alloy steel powder for powder metallurgy of the present invention at iron-based powder.
Here, as heat treated atmosphere, preferred reducing atmosphere, hydrogen atmosphere, preferred especially hydrogen atmosphere.In addition, can also be increased in the thermal treatment of carrying out under the vacuum.In addition, the thermal treatment temp that is fit to is 800～1200 ℃ a scope.Be preferably 800～1000 ℃.
In addition, when using iron powder under the atomizing state as iron-based powder, the content of C, O is high, therefore, and preferably through making thermal treatment in reducing atmosphere, reduce C and O.Through this reduction effect, the iron-based powder surface activation is even also can positively carry out being adhered to by what the diffusion that contains the Mo powder caused under low temperature (about 800 ℃～about 900 ℃).
Spread as described above and adhere to when handling, generally, iron-based powder with contain the Mo powder and behind sintering, become the caking state; Therefore; Through pulverizing/be classified to desired particle diameter, and further implement annealing as required, thereby process alloy steel powder for powder metallurgy.
In the present invention, the minuteness particle that preferably contains the Mo powder is equably attached to the iron-based powder surface.Under the situation of evenly not adhering to, handle the back alloy steel powder for powder metallurgy is pulverized, during transportation etc., contained the Mo powder to come off from the iron-based powder surface easily adhering to, what therefore increase unbound state especially easily contains the Mo powder.When sintering the Powdered Alloy Steel of this state into molding, there is the tendency of the dispersion state segregation of carbide.Therefore,, preferably make to contain the Mo powder, contain the Mo powder with what reduce the unbound state that produces owing to coming off etc. evenly attached to the surface of iron-based powder for intensity, the toughness that improves sintered compact.
The Mo amount that diffusion is adhered to is 0.05～1.5%.When less than 0.05% the time, it is little that carbide generates effect, and it is also little that intensity improves effect.On the other hand, when greater than 1.5% the time, carbide generates that effect is saturated, and organizing of sintered compact becomes inhomogeneous on the contrary, the effect of the intensity that therefore can not be improved.Therefore, the Mo amount that diffusion is adhered to is 0.05～1.5%.Be preferably 0.05～0.5% scope, more preferably 0.1～0.5% scope.Further be preferably 0.15～0.3%.
In addition, the surplus of Powdered Alloy Steel is iron and impurity.As the impurity that contains in the Powdered Alloy Steel, can enumerate C, O, N, S etc., as long as they respectively do for oneself below the C:0.02%, O:0.3% is following, N:0.004% is following, below the S:0.03%, then do not have special problem.O is preferably below 0.2%.
When above-mentioned Powdered Alloy Steel was made sintered compact as raw material, carbon dusts such as graphite were because effective aspect high strength and high-fatigue strengthization, and therefore, interpolation is counted 0.1～1.0% graphite with the C conversion and mixed before press molding.Above-mentioned C conversion amount is the quality ratio with respect to mixed Powdered Alloy Steel powder mix.
In addition, with regard to the present invention, certainly add the interpolation material that is used to improve characteristic according to purpose.For example, be purpose with the intensity of improving sintered compact, can illustration add Cu powder, Ni powder; With the machinability of improving sintered compact is purpose, can illustration adds machinability such as MnS and improves and use powder.
The impurity that contains in the Powdered Alloy Steel powder mix is as long as O:0.3% is following, N:0.004% is following, below the S:0.03%, then do not have special problem.O is preferably below 0.2%.But,, do not treating under the situation of on purpose adding as above-mentioned additive as impurity, therefore also there is no need to be controlled in the above-mentioned scope.
Then, preferred sintering condition describes when using alloy steel powder for powder metallurgy of the present invention to make sintered compact.
When press molding, can also the pulverous lubricant of additionally mixed.In addition, also can on mould, be coated with or adhere to lubricant.No matter under which kind of situation,, all can preferably use known lubricants such as amide-based wax such as metallic soap, ethylenebisstearamide such as Zinic stearas as lubricant.During hybrid lubricant, be about 0.1 mass parts～about 1.2 mass parts preferably with respect to Powdered Alloy Steel powder mix 100 mass parts.
When press molding, must under the pressure of 400～1000MPa, carry out.This be because, when pressure during less than 400MPa, the density of resulting molding reduces, thus the characteristic of sintered compact reduces; On the other hand, when greater than 1000MPa, the lost of life of mould, it is unfavorable to become economically.In addition, the temperature during pressurization is preferably normal temperature (about 20 ℃)～about 160 ℃ scope.
In addition, sintering must carry out in 1100～1300 ℃ TR.This be because, when sintering temperature was lower than 1100 ℃, sintering can't carry out, thus the characteristic of sintered compact reduces; On the other hand, when being higher than 1300 ℃, the lost of life of sintering oven, it is unfavorable to become economically.In addition, preferred sintering time is 10～180 minutes a scope.For make for the carbide that contains Nb and Mo at least separates out also preferred this sintering range and sintering time around the pore of agglomerated material.
For resulting sintered compact; Can implement intensified process such as carburizing and quenching, bright quenching, high-frequency quenching and nicarbing processing as required; Even but under the situation of not implementing intensified process, specific tenacity and toughness also improve mutually with existing sintered compact (not implementing the sintered compact of intensified process).Need to prove that each intensified process can be carried out through ordinary method.
State on the implementation under the agglomerating situation, form the high zone of Mo concentration, but owing to have carbide forming element and C such as Nb in this zone simultaneously, the carbide that therefore contains Mo and Nb etc. is separated out, disperseed at the sintering neck of iron-based powder intergranular.When separating out this carbide around the pore, the sintering neck is reinforced, and therefore can access intensity and all good tissue of toughness.
Show to Fig. 1 pattern the sintering structure that comprises the sintering neck of the sintered compact that obtains by the present invention.Among the figure, label 1 is that iron-based powder, 2 is the sintering neck around the pore.
Here,, can enumerate: (Nb, Mo) C, (Nb, V, Mo) C, (Nb, Ti, Mo) C and (Nb, Ti, V, Mo) C as the carbide that contains Mo and Nb etc.
In addition, preferred above-mentioned carbide is with per unit area 1 μ m
2In about 1～about 100 ratio separate out at the Mo of sintering neck rich region.Need to prove that the Mo rich region is meant the sintering neck zone of about 10 μ m on every side.
Embodiment
Below, through embodiment the present invention is described in further detail, but the present invention does not receive any restriction of following instance.
Embodiment 1
Through water atomization the molten steel of the alloying element shown in No.1～17 of containing table 1 is sprayed, process the iron-based powder of atomizing state.Ratio with predetermined adds oxidation Mo powder in this iron-based powder; And use V-Mixer to mix 15 minutes; Then; In dew point is 30 ℃ hydrogen atmosphere, heat-treat (keep temperature: 875 ℃, hold-time: 1 hour), the alloy steel powder for powder metallurgy of the Mo of predetermined amount has been adhered in the surface diffusion of making iron-based powder thus.
Then,, add the graphite of amount shown in the table 1, and then to add with respect to resulting Powdered Alloy Steel powder mix 100 mass parts be the ethylenebisstearamide of 0.6 mass parts, use V-Mixer to mix then 15 minutes these alloy steel powder for powder metallurgy.Then, under the pressure of 686MPa, carry out press molding, make the sheet-like formed body of long 55mm, wide 10mm, thick 10mm.
This sheet-like formed body is implemented sintering, process sintered compact.This sintering in N2-10%H2 atmosphere, sintering temperature: 1130 ℃, sintering time: carry out under 20 minutes the condition.
Be used under the situation of tension test; Use resulting sintered compact is processed into the pole tensile test specimen of parallel portion diameter as 5mm after; Carry out gas cementation (keep temperature: 870 ℃, hold-time: 60 minutes) for 0.8% time at carbon potential, quench then (60 ℃, oil quenching) and anneal (180 ℃, 60 minutes) and the test specimen that obtains; In addition; Be used under the situation of summer than (charpy) shock test; Use 0.8% time is carried out gas cementation (keep temperature: 870 ℃, hold-time: 60 minute) with the original shape of sintering state at carbon potential with resulting sintered compact, quenches then (60 ℃, oil quenching) and anneals (180 ℃, 60 minutes) and the test specimen that obtains.
Tensile strength TS (MPa) and impact value (J/cm with these sintered compacies
2) mensuration result be shown in table 1 in the lump.
Table 1
As shown in table 1, relatively invention example can know that with the tensile strength and the impact value of comparative example the invention example all can have HS and H.T. concurrently, that is, tensile strength is more than the 1150MPa, impact value is 10J/cm
2More than, and relative therewith, any ratio invention example in the tensile strength of any comparative example and the impact value is poor.
In addition, with regard to the present invention example, the SEM through the sintered compact cross section observes and image analysis, all at the per unit area 1 μ m of the Mo of sintering neck rich region
2In observed about 1～about 100 (Nb, Mo) C, (Nb, V, Mo) C, (Nb, Ti, Mo) C and (Nb, Ti, V, Mo) C etc.
Claims (6)
1. alloy steel powder for powder metallurgy, it is that the Mo powder that contains of 0.05～1.5 quality % adheres in the comminuted steel shot surface diffusion of the Nb of pre-alloyed 0.02～0.4 quality % and forms through making the Mo amount.
2. alloy steel powder for powder metallurgy, it is that at least any one the comminuted steel shot surface diffusion of Mo powder in the Ti of the V of the Nb of pre-alloyed 0.02～0.4 quality % and pre-alloyed 0.01～0.4 quality % and 0.01～0.4 quality % that contain of 0.05～1.5 quality % adhered to and formed through making the Mo amount.
3. iron based material through claim 1 or 2 described alloy steel powder for powder metallurgy press-powders being shaped, carrying out sintering then and obtain, around the pore of said agglomerated material, is separated out the carbide that contains Nb and Mo at least.
4. iron based material as claimed in claim 3, wherein, the said carbide that contains Nb and Mo at least for (Nb, Mo) C, (Nb, V, Mo) C, (Nb, Ti, Mo) C and (Nb, Ti, V, Mo) among the C at least any one.
5. the method for manufacture of an iron based material; It is characterized in that; Claim 1 or 2 described alloy steel powder for powder metallurgy are mixed with the carbon dust of 0.1～1.0 quality %; Under the pressure of 400～1000MPa, carry out press-powder then and be shaped, under 1100～1300 ℃ temperature, carry out sintering then, make the pore of the agglomerated material of gained separate out the carbide that contains Nb and Mo at least on every side.
6. the method for manufacture of iron based material as claimed in claim 5, wherein, the said carbide that contains Nb and Mo at least for (Nb, Mo) C, (Nb, V, Mo) C, (Nb, Ti, Mo) C and (Nb, Ti, V, Mo) among the C at least any one.
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| CN112041103A (en) * | 2019-01-30 | 2020-12-04 | 住友电气工业株式会社 | Sintered material and method for producing sintered material |
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| EP0302430A1 (en) * | 1987-08-01 | 1989-02-08 | Kawasaki Steel Corporation | Alloyed steel powder for powder metallurgy |
| JPH0681001A (en) * | 1992-09-02 | 1994-03-22 | Kawasaki Steel Corp | Alloy steel powder |
| JPH07138694A (en) * | 1993-11-15 | 1995-05-30 | Kobe Steel Ltd | Production of low alloy steel powder for powder metallurgy and ferrous sintered parts with high dimensional accuracy |
| CN1342780A (en) * | 2000-08-31 | 2002-04-03 | 川崎制铁株式会社 | Alloy steel powder for powder metallurgy |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110267754A (en) * | 2017-02-02 | 2019-09-20 | 杰富意钢铁株式会社 | The manufacturing method of powder used in metallurgy mixed powder, sintered body and sintered body |
| 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 |
| CN112041103A (en) * | 2019-01-30 | 2020-12-04 | 住友电气工业株式会社 | Sintered material and method for producing sintered material |
Also Published As
| Publication number | Publication date |
|---|---|
| JP5929084B2 (en) | 2016-06-01 |
| JP2012140699A (en) | 2012-07-26 |
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