CN105555440A - Alloy steel powder for powder metallurgy and method of producing iron-based sintered body - Google Patents
Alloy steel powder for powder metallurgy and method of producing iron-based sintered body Download PDFInfo
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- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
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- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
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- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/05—Metallic powder characterised by the size or surface area of the particles
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- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/10—Metallic powder containing lubricating or binding agents; Metallic powder containing organic material
- B22F1/107—Metallic powder containing lubricating or binding agents; Metallic powder containing organic material containing organic material comprising solvents, e.g. for slip casting
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
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- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/17—Metallic particles coated with metal
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- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
- B22F3/16—Both compacting and sintering in successive or repeated steps
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- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
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- 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
- C22C33/0264—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements the maximum content of each alloying element not exceeding 5%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
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- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- 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
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2301/00—Metallic composition of the powder or its coating
- B22F2301/35—Iron
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2304/00—Physical aspects of the powder
- B22F2304/10—Micron size particles, i.e. above 1 micrometer up to 500 micrometer
Abstract
According to the present invention, an alloy steel powder for powder metallurgy is regulated to have a specific surface area of 0.100 m2/g or larger, contain Mo in an amount in the range of 0.2-1.5 mass%, and contain a graphite powder in an amount in the range of 0.1-1.0 mass% per 100 mass% the alloy steel powder for powder metallurgy. Thus, a sintered body which combines strength and toughness on a high level can be obtained from the alloy steel powder for powder metallurgy.
Description
Technical field
The present invention relates to the alloy steel powder for powder metallurgy being suitable for PM technique, especially seek to improve intensity and the toughness of the agglomerated material employing described powdered alloy steel.
In addition, the present invention relates to the manufacture method of the iron base sintered body of intensity and the tenacity excellent using above-mentioned alloy steel powder for powder metallurgy to make.
Background technology
PM technique is due to can manufacture the parts of complicated shape, so can significantly reduce cutting cost with article shape shape closely (so-called near net-shaped shape (nearnetshape)) with high dimensional accuracy.Therefore, sintered metal product is used in a lot of field as various frame for movement thing or its parts.
In addition, recently, in order to realize miniaturization, the lightweight of parts, the strong intensity expecting raising sintered metal product, especially, the requirement for the high strength of iron-based powder goods (iron base sintered body) is strong.
As the iron-based powder for powder metallurgy formed body of the last stage of iron base sintered body usually by with under type manufacture: mix the alloy such as copper powder, graphite powder powder and the lubricant such as stearic acid, zinc stearate and make iron-based powder mixed powder in iron-based powder, fill it in mould, carry out extrusion forming, manufacture thus.And different according to composition, iron-based powder can be classified as iron powder (such as straight iron powder etc.), powdered alloy steel etc.In addition, based in the classification of method for making, comprise atomized iron powder (atomizedironpowder), reduced iron powder etc., this word of the iron powder in above-mentioned classification uses with the broad sense comprising powdered alloy steel.
The density of the iron-based powder for powder metallurgy formed body obtained by common powder metallurgy operation is generally 6.8 ~ 7.3Mg/m
3left and right.For this iron-based powder formed body, implement sintering processes subsequently and form iron base sintered body, and then implementing pressure-sizing processing (sizing), machining etc. as required, forming sintered metal product.In addition, when needs more high strength, sometimes also implement carburizing heat treatment, brightness heat treatment after sintering.
Herein, all the time, the powder obtained as the stage interpolation alloying element in raw meal, there will be a known following powder of Denging:
(1) in straight iron powder, each alloying element powder is coordinated and the mixed powder obtained;
(2) the prealloy comminuted steel shot complete for each element alloying obtained;
(3) make each alloying element powder partly spread on the surface of straight iron powder, prealloy comminuted steel shot and obtain diffusion attachment powdered alloy steel.
The mixed powder coordinating each alloying element powder in straight iron powder shown in above-mentioned (1), has the advantage can guaranteeing the high-compressibility suitable with straight iron powder.But, there is following such problem: because the segregation of each alloying element powder is large, so the deviation of characteristic is large, in addition, alloying element does not fully spread in Fe, becomes the state of heterogeneous structure, cannot reach effective matrix strengthening.
Therefore, above-mentionedly in straight iron powder, coordinate each alloying element powder and the mixed powder obtained cannot tackle the requirement of stability of characteristics in recent years, high strength, its use amount reduces gradually.
In addition, shown in above-mentioned (2) is material molten steel atomization manufactured by the prealloy comminuted steel shot of complete for each element alloying, although it can reach the matrix strengthening based on uniform formation, the compressibility caused because of solution hardening effect reduces and becomes problem.
In addition, diffusion attachment powdered alloy steel shown in above-mentioned (3) is the metal dust coordinating each element in straight iron powder, prealloy comminuted steel shot, and heat under the atmosphere of non-oxidizable or reproducibility, thus on the surface of straight iron powder, prealloy comminuted steel shot partly each metal dust of diffusion bond manufacture, therefore, the advantage of the iron base powder mixture of above-mentioned (1) and the prealloy comminuted steel shot of above-mentioned (2) can be had concurrently.
Therefore, the segregation of alloying element can prevented, and while guaranteeing the high-compressibility suitable with straight iron powder, the complex tissue being dispersed with alloy part enrichment phase can formed, therefore there is the possibility of matrix strengthening, develop as the diffusion attachment powdered alloy steel for high strength object.
As mentioned above, in order to improve intensity, the toughness of sintered metal product, high-alloying can be considered.But in this alloying, harden as raw-material powdered alloy steel, compressibility reduces, the facility load produced in extrusion forming increases such problem.In addition, the reduction of the compressibility of powdered alloy steel causes the density of sintered body to reduce, and will offset high strength.That is, in order to improve intensity, the toughness of sintered metal product, the technology making sintered body high strength while doing one's utmost to suppress compressibility to reduce is required.
As the technology making sintered body high strength while maintaining compressibility as described above, usually carry out following operation: added in iron-based powder by alloying elements such as improving Ni, Cu and Mo of hardenability (hardenability).As to the effective element of this object, such as, Patent Document 1 discloses following technology: by adding in iron powder by Mo as prealloy element using the scope not damaging compressibility (Mo:0.1 ~ 1.0 quality %), and then make Cu and Ni diffusion attachment on the particle surface of this iron powder in the form of a powder, thus realize simultaneously press-powder shaping time compressibility and sintering after the intensity of component.
In addition, propose in patent document 2 make alloying element of more than two kinds, especially Mo and Ni or add Cu iron and steel powder spread on the surface attachment the alloy steel powder for powder metallurgy for high-strength sintered body.
This technology also proposed and controls each diffusion attachment element, with make relative to particle diameter be the particulate powder of less than 44 μm diffusion attachment concentration drop on relative to this iron and steel powder entirety diffusion attachment concentration the scope of 0.9 ~ 1.9 times in, thinking by being limited in this wider scope, the impact flexibility of sintered body can be guaranteed.
On the other hand, before this, also proposed and be main alloy element with Mo and not containing the Mo system powdered alloy steel of Ni, Cu.Such as, in patent document 3, the acceleration of sintering in order to the α forming the fast Fe of self diffusion velocity is single-phase, proposes and comprises the powdered alloy steel of ferrite stabilizer Mo as prealloy using the scope of 1.5 ~ 20 quality %.For this powdered alloy steel, thinking by making domain size distribution etc. be suitable for the such operation of pressure sintering, highdensity sintered body can be obtained, in addition, thinking by not using the alloying element spreading attached type, even and stable tissue can be obtained.
Similarly, as the alloy steel powder for powder metallurgy taking Mo as main alloy element, technology disclosed in patent document 4 is had.This technology proposes and makes the Mo of 0.2 ~ 10.0 quality % on the surface of iron-based powder, spread attachment and the powdered alloy steel that obtains, described iron-based powder contain below 1.0 quality % Mn or further containing being less than the Mo of 0.2 quality % as prealloy.Iron-based powder can use atomized iron powder, also can use reduced iron powder in addition, thinks that it is suitable for making average grain diameter be 30 ~ 120 μm.And think, this powdered alloy steel not only compressibility is excellent, and can obtain high density and the sintered component of high strength.
Prior art document
Patent document
Patent document 1: Japanese Patent Publication 63-66362 publication
Patent document 2: Japanese Laid-Open Patent Publication 61-130401 publication
Patent document 3: Japanese Patent Publication 6-89365 publication
Patent document 4: Japanese Unexamined Patent Publication 2002-146403 publication
Summary of the invention
Invent problem to be solved
But, in the technology recorded in patent document 1 and 2, using Ni as required adding ingredient, but due to Ni diffusion when sintering slow, so in order to make Ni fully spread in iron powder, iron and steel powder, need to sinter for a long time.
In addition, in the technology recorded in patent document 3, Mo addition is higher, and be more than 1.8 quality %, compressibility is low, thus there is the shortcoming that cannot obtain high compact density.Therefore, when applying common sintering circuit (do not carry out carry out with pressurizeing 1 time sintering), there is the product that can only obtain low frit density and can not get the such problem of sufficient intensity, toughness.
In addition, the technology recorded in patent document 4 is the technology of the recompression being suitable for comprising sintered body and the powder metallurgy operation sintered again.That is, have and cannot give full play to the such problem of aforesaid effect in common sintering process.
As a result, found by the research of inventing people, employ the sintered body of any one powdered alloy steel recorded in above-mentioned patent document 1 ~ 4, be all difficult to realize intensity and toughness at a high level simultaneously.
The present invention develops in view of above-mentioned present situation, its object is to the problem overcoming above-mentioned prior art, a kind of alloy steel powder for powder metallurgy is proposed, use this alloy steel powder for powder metallurgy, intensity and the toughness of the sintered body employing this alloy steel powder for powder metallurgy can be realized at a high level simultaneously.
For solving the means of problem
In order to reach above-mentioned purpose, invention people have carried out various research repeatedly to the alloying component of iron-based powder and adding means thereof, and result obtains opinion as described below.
That is, following opinion is obtained: be used in iron-based powder and adhere to the alloy steel powder for powder metallurgy obtained containing Mo alloy powder on the surface, and the specific area of described alloy steel powder for powder metallurgy is 0.100m
2/ more than g and containing the Mo of 0.2 ~ 1.5 quality % in described alloy steel powder for powder metallurgy, by using such alloy steel powder for powder metallurgy, thus this powdered alloy steel is carried out shaping, sintering time, its agglutinating property is excellent, therefore, the pore appropriateness miniaturization of sintered body, the intensity of sintered body and the toughness of sintered body all improve.
The present invention completes based on above-mentioned opinion.
That is, main composition of the present invention is as described below.
1. an alloy steel powder for powder metallurgy, it adheres to and obtains containing Mo alloy powder on the surface of iron-based powder, and wherein, the specific area of this alloy steel powder for powder metallurgy is 0.100m
2/ more than g, and the Mo amount in this alloy steel powder for powder metallurgy is the scope of 0.2 ~ 1.5 quality %, and then, relative to this alloy steel powder for powder metallurgy 100 quality %, contain graphite powder with the scope of 0.1 ~ 1.0 quality %.
2. the alloy steel powder for powder metallurgy as described in above-mentioned 1, wherein, relative to this alloy steel powder for powder metallurgy 100 quality %, contains Cu powder with the scope of 0.5 ~ 4.0 quality % further.
3. the alloy steel powder for powder metallurgy as described in above-mentioned 1 or 2, wherein, described iron-based powder contains reduced iron powder, and the average grain diameter of this iron-based powder is less than 80 μm.
4., as the alloy steel powder for powder metallurgy according to any one of above-mentioned 1 ~ 3, wherein, the oxygen content of described iron-based powder is below 0.3 quality %.
5. a manufacture method for iron base sintered body, it is in the alloy steel powder for powder metallurgy according to any one of above-mentioned 1 ~ 4, adds lubricant and mixes, then carrying out extrusion forming process, sintering processes, forms iron base sintered body.
The effect of invention
By according to alloy steel powder for powder metallurgy of the present invention, owing to not needing to use Ni, and compressibility is high, even if so utilize common sintering process, also can obtain the agglomerated material having high strength and high tenacity concurrently at an easy rate.
Detailed description of the invention
Below, the present invention is illustrated.
Alloy steel powder for powder metallurgy of the present invention is the alloy steel powder for powder metallurgy that attachment obtains containing Mo alloy powder on the surface of iron-based powder, and it is characterized in that, the specific area of powdered alloy steel is 0.100m
2/ more than g, the Mo amount in powdered alloy steel is the scope of 0.2 ~ 1.5 quality %.
And, by above-mentioned alloy steel powder for powder metallurgy is mixed with appropriate powdered graphite as follows, form formed body, sinter, make the pore miniaturization effectively of sintered body thus, intensity can be obtained, sintered component that toughness all improves.
For by the invention enables the pore of sintered body effectively miniaturization thus intensity can be obtained, the mechanism of sintered component that toughness improves, invention people consider as follows.
Usually, there is a large amount of pores in sintered body, therefore there is stress and concentrate at air cap, the tendency that the intensity of sintered body, toughness reduce.But, for for alloy steel powder for powder metallurgy of the present invention, be 0.100m by making the specific area of powdered alloy steel
2/ more than g, thus the pore miniaturization making sintered body, the degree that stress is concentrated relaxes, and makes sintered neck Strengthening and Toughening.
In addition, be the scope of 0.2 ~ 1.5 quality % by making the Mo in powdered alloy steel, thus Mo is in the pore periphery enrichment of sintered body, not only sintered body is strengthened further, and, for for alloy steel powder for powder metallurgy of the present invention, owing to being attached with containing Mo alloy powder on the surface of iron-based powder, and at matrix part not containing Mo, so compared with sintered neck, be not easy Formed compound, form the tissue of high tenacity.
That is, can think, control by distributing to the gas cell distribution of sintered body and Mo, making the present invention can realize high strength and the high tenacity of sintered body simultaneously.
Below, the restriction reason of limitation of the invention item is described.
First, the manufacture method of alloy steel powder for powder metallurgy of the present invention is described.
In the present invention, prepare the iron powder such as atomized iron powder, reduced iron powder as iron-based powder, and, prepare the Mo material powder as the raw material containing Mo alloy powder.
As above-mentioned iron-based powder, usually, as long as can be used for the iron-based powder in powder metallurgic method, be not particularly limited, preferred so-called atomization fecula, atomized iron powder or reduced iron powder.As atomised iron based powders, can for molten steel be atomized and carrying out any one in drying, the atomization fecula of classification, the atomized iron powder that atomization fecula reduced under reducing atmosphere.
In addition, reduced iron powder preferably uses the reduced iron powder reducing to the mill tap (millscale) generated when manufacturing steel, iron ore and obtain.It should be noted that, as the apparent density of reduced iron powder, as long as be 1.7Mg/m
3~ 3.0Mg/m
3left and right.Be more preferably 2.2 ~ 2.8Mg/m
3.Herein, apparent density refers to the density utilizing the test method of JISZ2504 to record.
On the other hand, as aforesaid Mo material powder, what can be used as target contains Mo alloy powder itself, also can use the compound of the Mo that can be reduced into containing Mo alloy powder.It should be noted that, the average grain diameter of Mo material powder is less than 50 μm, is preferably less than 20 μm.Herein, average grain diameter refers to volume to be the median particle diameter (so-called d50) of benchmark.
In addition, as containing Mo alloy powder, with the pure metal powder of Mo for representative, Mo alloy powder such as oxidation Mo powder or Fe-Mo (molybdenum-iron, ferromolybdenum) powder etc. advantageously can be applied.On the other hand, as the compound of Mo, Mo carbide, Mo sulfide, Mo nitride etc. can be enumerated.
Next, with the ratio specified, above-mentioned iron-based powder and the mixing of Mo material powder are formed mixed powder, regulate this ratio to measure to make the Mo in alloy steel powder for powder metallurgy the scope finally becoming 0.2 ~ 1.5 quality %.In addition, when mixing, mixed method, mixing apparatus being not particularly limited, such as, can using Henschel mixer (Henschelmixer), cone-type mixer (conemixer) etc., conventionally carry out.
Further, at high temperature keep this mixed powder, at the contact surface place of iron-based powder and Mo material powder, Mo spread in iron and carries out engaging (diffusion attachment process), alloy steel powder for powder metallurgy of the present invention can be obtained thus.
As the atmosphere of above-mentioned diffusion attachment process, preferred reducing atmosphere, hydrogeneous atmosphere, particularly preferably hydrogen atmosphere.It should be noted that, also can implement heat treatment under vacuo.In addition, the temperature of preferred diffusion attachment process is the scope of 800 ~ 1000 DEG C.
When carrying out diffusion attachment process as described above, usually, iron-based powder with containing Mo sintering alloy powder and become the state of solidifying, therefore, carry out pulverizing and classification to become desired particle diameter.In addition, annealing can be implemented as required.It should be noted that, as the particle diameter of alloy steel powder for powder metallurgy, be preferably less than 180 μm.
In the present invention, be preferably attached to iron-based powder equably on the surface containing Mo alloy powder.When evenly not adhering to, after alloy steel powder for powder metallurgy being carried out to diffusion attachment process, carry out pulverizing, when carrying out carrying etc., easily come off from iron-based powder surface, thus especially easily the increasing containing Mo alloy powder of free state.When by shaping for the powdered alloy steel of such state, sintering, the dispersity of carbide produces segregation.Therefore, in order to improve intensity, the toughness of sintered body, preferably make to be attached to equably on the surface of iron-based powder containing Mo alloy powder, reduce the free state produced owing to come off etc. containing Mo alloy powder.
The Mo amount that diffusion in alloy steel powder for powder metallurgy is adhered to is the scope of 0.2 ~ 1.5 quality % (interior number).Its reason is, during lower than 0.2 quality %, it is little that hardenability improves effect, strength-enhancing effect is also little, on the other hand, during more than 1.5%, it is saturated that hardenability improves effect, and the inhomogeneities of the tissue of sintered body increases on the contrary, therefore cannot obtain high strength and high tenacity.Therefore, the Mo amount making the diffusion in powdered alloy steel adhere to is the scope of 0.2 ~ 1.5 quality %.Be preferably the scope of 0.3 ~ 1.0 quality %.
On the other hand, the powdered alloy steel of attachment is spread for the Mo that makes used in the present invention, its specific area is defined as 0.100m
2/ more than g.Be preferably 0.150m
2/ more than g.Its reason is, specific area is less than 0.100m
2during/g, because reactivity when there is thick pore or sintering is insufficient, or due to above-mentioned two reasons, thus cause the miniaturization of pore not carried out, toughness reduces.The upper limit of specific area is not particularly limited, but more than 0.5m
2during/g, will containing a large amount of micro mist, compressibility reduces, and is thus preferably 0.5m
2/ below g.
In addition, by carrying out diffusion attachment process to Mo on the surface at iron-based powder, thus the specific area of powder reduces, therefore, from this point to consider, based on the specific area of iron-based powder be preferably 0.150m
2/ more than g.It should be noted that, the specific area in the present invention utilizes gas adsorption method (BET method) to record.
In the present invention, the remainder of powdered alloy steel is iron and inevitable impurity.As the impurity contained in powdered alloy steel, C, O, N and S etc. can be enumerated, for their content, in powdered alloy steel, as long as be respectively below C:0.02 quality %, O:0.3 below quality %, below N:0.004 quality % and S:0.03 below quality %, just do not have special problem, O is more preferably below 0.25 quality %.Its reason is, when the amount of inevitable impurity exceedes above-mentioned scope, the compressibility of powdered alloy steel reduces, and is the preform with sufficient density by being difficult to compression forming.
Using above-mentioned composite alloy comminuted steel shot as in the alloy steel powder for powder metallurgy of principal component, according to the ratiometer relative to alloy steel powder for powder metallurgy entirety (100 quality %), with the scope of 0.1 ~ 1.0 quality % add graphite powder be important.In addition, in the present invention, according to the ratiometer relative to alloy steel powder for powder metallurgy entirety (100 quality %), the Cu powder of 0.5 ~ 4.0 quality % can be added.
C as the principal component of graphite powder is solid-solution in iron when sintering, and can realize solution strengthening, hardenability raising etc., is for the useful element of the intensity improving sintered component.In the present invention, utilize carburizing heat treatment etc. externally in sintered body when carburizing after sintering, the quantity of graphite of interpolation can be a small amount of, if but less than 0.1 quality %, then above-mentioned additive effect is not enough.On the other hand, under not carrying out the heat treated situation of carburizing when sintering, add graphite powder, if but more than 1.0 quality %, then hypereutectoid will occur, therefore, cementite is separated out, and causes intensity to reduce.Therefore, graphite powder is limited in the scope of 0.1 ~ 1.0 quality %.It should be noted that, the average grain diameter of graphite powder is preferably less than 50 μm.
On the other hand, Cu is the useful element with following effect: by solution strengthening, the hardenability raising of iron-based powder, thus improve the intensity of sintered component; Cu also has following effect: the melting when carrying out the sintering of iron-based powder and become liquid phase, and the particle of iron-based powder is bonded mutually.But when addition is less than 0.5 quality %, its additive effect is not enough, and on the other hand, during more than 4.0 quality %, not only the strength-enhancing effect of sintered component is saturated, and causes machinability to reduce.Therefore, Cu powder is preferably the scope of 0.5 ~ 4.0 quality %.Be more preferably the scope of 1.0 ~ 3.0 quality %.It should be noted that, the average grain diameter of Cu powder is preferably less than 50 μm.
The iron-based powder used in the present invention preferably contains reduced iron powder and average grain diameter is less than 80 μm.This is because if more greatly, namely average grain diameter contains the large powder of particle diameter more than 80 μm, then driving force when sintering dies down, and forms thick hole around thick iron-based powder.And, this thick hole become make sintered body intensity, toughness reduce reason.
Herein, above-mentioned average grain diameter refers to quality to be the median particle diameter (so-called d50) of benchmark.Specifically, use in JISZ8801 the sieve specified to sieve, measure the quality of sample residual on each sieve, try to achieve particle diameter smaller side and particle diameter larger side is that the particle diameter of equivalent is as median particle diameter.
In the present invention, according to object, the additive for improving characteristic can be added.Such as, for the object of intensity improving sintered body, can suitably adding Ni powder, in addition, for the object of machinability improving sintered body, suitably can adding the powder for improving machinability such as MnS.It should be noted that, according to the ratiometer relative to iron(-)base powder entirety (100 quality %), preferably make Ni powder be the scope of 0.5 ~ 5 quality %.
On the other hand, MnS etc. can be in the past known additions for improving the addition of the powder of machinability, that is, according to the ratiometer relative to iron(-)base powder entirety (100 quality %), can be about 0.1 ~ 1 quality %.
And then, preferred condition of molding, sintering condition during use alloy steel powder for powder metallurgy manufacture of the present invention sintered body are described.
When carrying out the extrusion forming employing alloy steel powder for powder metallurgy of the present invention, also can the pulverous lubricant of additional mixing.In addition, also can be coated with on mould or adhere to lubricant and carry out shaping.No matter in any situation, as lubricant, any lubricant in the acid amides system wax such as the metallic soap such as zinc stearate, lithium stearate, ethylene bis stearamide (ethylenebisstearamide) and other known lubricants all can be used suitably.It should be noted that, when hybrid lubricant, preferably, relative to alloy steel powder for powder metallurgy 100 mass parts, about making the amount of lubricant be 0.1 ~ 1.2 mass parts (outside add).
When by alloy steel powder for powder metallurgy extrusion forming of the present invention, preferably carry out with the plus-pressure of 400 ~ 1000MPa.This is because when plus-pressure is less than 400MPa, the density step-down of the formed body obtained, the characteristic of sintered body reduces, and on the other hand, during more than 1000MPa, the lifetime of mould, it is unfavorable to become economically.It should be noted that, preferably make temperature during pressurization be the scope of normal temperature (about 20 DEG C) ~ about 160 DEG C.
In addition, the sintering of alloy steel powder for powder metallurgy of the present invention preferably carries out in the temperature range of 1100 ~ 1300 DEG C.This is because when sintering temperature is lower than 1100 DEG C, sintering does not carry out, the characteristic of sintered body reduces, and on the other hand, during more than 1300 DEG C, the lifetime of sintering furnace, it is unfavorable to become economically.It should be noted that, preferably make sintering time be the scope of 10 ~ 180 minutes.
For the sintered body obtained, as required, the intensive treatment such as carburizing and quenching, bright quenching, high-frequency quenching and nicarbing process can be implemented, even if but when not implementing intensive treatment, for the sintered body employed according to alloy steel powder for powder metallurgy of the present invention, compared with existing sintered body (not implementing the sintered body of intensive treatment), its intensity and toughness are also improved.It should be noted that, each intensive treatment is conventionally implemented.
Embodiment
Below, in further detail the present invention is described by embodiment, but the present invention is not by any restriction of following example.
In the present embodiment, as iron-based powder, employing apparent density is 2.65Mg/m
3or apparent density is 2.80Mg/m
3, apparent density is 3.25Mg/m
3atomization fecula, employing apparent density is in addition 2.60Mg/m
3or apparent density is 2.75Mg/m
3reduced iron powder, in addition, employing apparent density is 2.60Mg/m
3or apparent density is 2.80Mg/m
3, apparent density is 3.30Mg/m
3atomized iron powder.
In these iron-based powders, oxidation Mo powder (average grain diameter: 10 μm) is added with the ratio of regulation, V-Mixer is utilized to mix 15 minutes, then, be heat-treat (keep temperature: 880 DEG C, retention time: 1h) in the hydrogen atmosphere of 30 DEG C at dew point, on the surface being manufactured on iron-based powder, diffusion is attached with the alloy steel powder for powder metallurgy of the Mo of the ormal weight shown in table 1.
Next, to in these alloy steel powder for powder metallurgy, add copper powder (average grain diameter: 30 μm), the graphite powder (average grain diameter: 5 μm) of the amount shown in table 1, and then, relative to these iron-based powder mixed powder 100 mass parts, add 0.6 mass parts ethylene bis stearamide, then utilize V-Mixer to mix 15 minutes.Next, 7.0Mg/m is become with the density of formed body
3mode carry out extrusion forming, make sheet (tabletshaped) formed body of long 55mm, wide 10mm, thick 10mm.
Sintering is implemented to this sheet-like formed body, makes sintered body.It should be noted that, this sintering is in transformation of propane gas atmosphere, sintering temperature be 1130 DEG C, sintering time carries out under being the condition of 20 minutes.
Next, the sintered body obtained is processed into the pole shape tension test sheet that parallel portion diameter is 5mm, for the tension test specified in JISZ2241.In addition, when summer ratio (Charpy) impact test specified in for JISZ2242, employ the test material obtained as follows: the sintered body obtained directly is carried out with the shape after sintering the gas carburizing (keeping temperature: 870 DEG C, retention time: 60 minutes) that carbon potential is 0.8 quality %, then carry out quenching (60 DEG C, oil hardening) and tempering (180 DEG C, 60 minutes), thus obtain test material.
For these sintered bodies, the Charpy-type test specified in the tension test and JISZ2242 specified in JISZ2241 is utilized to measure tensile strength (MPa) and impact value (J/cm
2).Each measurement result merging is shown in table 1.
[table 1]
As shown in table 1, when comparing the tensile strength of example and comparative example and impact value, the tensile strength of example is all shown as more than 1000MPa, and impact value is all shown as 14.0J/cm
2above, can realize intensity and toughness at a high level, on the other hand, the impact value of comparative example is all less than 14.0J/cm simultaneously
2, at least either side in tensile strength and impact value is poorer than example.
It should be noted that, in table 1, also show the result of the 4Ni material (4Ni-1.5Cu-0.5Mo, the maximum particle diameter of raw meal: 180 μm) as current material.Known example can obtain the characteristic more excellent than existing 4Ni material.
Claims (5)
1. an alloy steel powder for powder metallurgy, it adheres to and obtains containing Mo alloy powder on the surface of iron-based powder, and wherein, the specific area of described alloy steel powder for powder metallurgy is 0.100m
2/ more than g, and the Mo amount in described alloy steel powder for powder metallurgy is the scope of 0.2 ~ 1.5 quality %, and then, relative to described alloy steel powder for powder metallurgy 100 quality %, contain graphite powder with the scope of 0.1 ~ 1.0 quality %.
2. alloy steel powder for powder metallurgy as claimed in claim 1, wherein, relative to described alloy steel powder for powder metallurgy 100 quality %, contains Cu powder with the scope of 0.5 ~ 4.0 quality % further.
3. alloy steel powder for powder metallurgy as claimed in claim 1 or 2, wherein, described iron-based powder contains reduced iron powder, and the average grain diameter of described iron-based powder is less than 80 μm.
4. the alloy steel powder for powder metallurgy according to any one of claims 1 to 3, wherein, the oxygen content of described iron-based powder is below 0.3 quality %.
5. a manufacture method for iron base sintered body, it is in the alloy steel powder for powder metallurgy according to any one of Claims 1 to 4, adds lubricant and mixes, then carrying out extrusion forming process, sintering processes, forms iron base sintered body.
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| JP2013200039 | 2013-09-26 | ||
| JP2013-200039 | 2013-09-26 | ||
| PCT/JP2014/004383 WO2015045273A1 (en) | 2013-09-26 | 2014-08-26 | Alloy steel powder for powder metallurgy, and process for producing iron-based sintered object |
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| CN105555440A true CN105555440A (en) | 2016-05-04 |
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| US (1) | US20160214171A1 (en) |
| JP (1) | JP5949952B2 (en) |
| KR (1) | KR20160045825A (en) |
| CN (1) | CN105555440A (en) |
| CA (1) | CA2922018C (en) |
| SE (1) | SE540965C2 (en) |
| WO (1) | WO2015045273A1 (en) |
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| CN111432957A (en) * | 2017-12-05 | 2020-07-17 | 杰富意钢铁株式会社 | Alloy steel powder |
| CN111432958A (en) * | 2017-12-05 | 2020-07-17 | 杰富意钢铁株式会社 | Partially diffused alloyed steel powder |
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| JP6428909B2 (en) * | 2015-09-18 | 2018-11-28 | Ｊｆｅスチール株式会社 | Iron-based sintered body and method for producing the same |
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Also Published As
| Publication number | Publication date |
|---|---|
| JP5949952B2 (en) | 2016-07-13 |
| SE540965C2 (en) | 2019-01-29 |
| WO2015045273A8 (en) | 2016-01-21 |
| US20160214171A1 (en) | 2016-07-28 |
| JPWO2015045273A1 (en) | 2017-03-09 |
| CA2922018A1 (en) | 2015-04-02 |
| CA2922018C (en) | 2018-01-16 |
| WO2015045273A1 (en) | 2015-04-02 |
| KR20160045825A (en) | 2016-04-27 |
| SE1650273A1 (en) | 2016-03-02 |
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