EP2511031A1 - Sintermetallurgiezusammensetzung und gesinterte Komponente - Google Patents

Sintermetallurgiezusammensetzung und gesinterte Komponente Download PDF

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EP2511031A1
EP2511031A1 EP11162124A EP11162124A EP2511031A1 EP 2511031 A1 EP2511031 A1 EP 2511031A1 EP 11162124 A EP11162124 A EP 11162124A EP 11162124 A EP11162124 A EP 11162124A EP 2511031 A1 EP2511031 A1 EP 2511031A1
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Prior art keywords
weight
component
powder
stainless steel
composition
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EP11162124A
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English (en)
French (fr)
Inventor
Sven Allroth
Ulf Engström
Ola Bergman
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Hoganas AB
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Hoganas AB
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Priority to EP11162124A priority Critical patent/EP2511031A1/de
Priority to PCT/EP2012/056544 priority patent/WO2012140057A1/en
Publication of EP2511031A1 publication Critical patent/EP2511031A1/de
Withdrawn legal-status Critical Current

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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
    • 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
    • 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
    • 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
    • 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
    • B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
    • B22F5/008—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product of engine cylinder parts or of piston parts other than piston rings
    • 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
    • C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
    • C22C33/0285—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with Cr, Co, or Ni having a minimum content higher than 5%
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05D—INDEXING SCHEME FOR ASPECTS RELATING TO NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES, GAS-TURBINES OR JET-PROPULSION PLANTS
    • F05D2220/00—Application
    • F05D2220/40—Application in turbochargers
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05D—INDEXING SCHEME FOR ASPECTS RELATING TO NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES, GAS-TURBINES OR JET-PROPULSION PLANTS
    • F05D2230/00—Manufacture
    • F05D2230/20—Manufacture essentially without removing material
    • F05D2230/22—Manufacture essentially without removing material by sintering
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
    • F05D—INDEXING SCHEME FOR ASPECTS RELATING TO NON-POSITIVE-DISPLACEMENT MACHINES OR ENGINES, GAS-TURBINES OR JET-PROPULSION PLANTS
    • F05D2300/00—Materials; Properties thereof
    • F05D2300/10—Metals, alloys or intermetallic compounds
    • F05D2300/17—Alloys
    • F05D2300/171—Steel alloys

Definitions

  • the present invention concerns a method of making a sintered components and the component made by the method.
  • Examples of such components are parts in turbochargers for internal combustion engines.
  • Iron-based powder compositions for powder metallurgical production of pressed and sintered component are often alloyed with carbon and copper.
  • Other alloying elements are also commonly used.
  • the alloying elements may be added according to various methods.
  • the alloying elements may be mixed with the iron-powder, carbon in the form of graphite is commonly added in this way. Such compositions may be called premixes.
  • the alloying elements may also be added to the melt prior to the atomisation process.
  • Iron-based powders produced according to this method are commonly referred to as pre-alloyed iron-based powders.
  • the alloying elements may also be attached to the surface of the iron-based powder by a thermal diffusion bonding process. Such powders are referred to as diffusion bonded powders.
  • the alloying elements may be attached to the surface of the iron-based powder by various binders. Such powders are commonly referred to as bonded powders or bonded mixtures.
  • sintered articles are manufactured from iron powder mixed with copper and graphite powders.
  • Other types of materials suggested include iron powder prealloyed with nickel, chromium and molybdenum and small amounts of manganese to enhance hardenability without developing stable oxides.
  • machining of the sintered component is unavoidable. In order to facilitate the machining process, machinability enhancing agents such as MnS may be added to the iron-based powder composition.
  • the components For iron-based pressed and sintered components which are subjected to wear and corrosion and elevated temperature a prerequisite in order to withstand such conditions is that the components contain suitable alloying elements. High sintered density, i.e. low porosity is also necessary. Examples of such components are components in turbochargers, such as unison or nozzle rings and sliding nozzles. In these cases a porosity less than 10 %, preferably less than 7% is needed. For some applications the components have to be gas tight. Today, unison or nozzle rings and sliding nozzles are often made from castings of alloyed iron-based material containing MnS phases, the presence thereof rendering a machinability enhancing effect.
  • the powder metallurgical production route is very suitable for producing such components as they are often produced in large quantities and the components have a suitable size.
  • the dimensional scatter between components have to be small and within a certain tolerance level, in order to avoid costly machining processes.
  • machining can not always be avoided why the addition of machining enhancing agents to the iron-based powder composition may be needed, however, such additions should not to any larger extent negatively influence other properties such as strength, wear -, creep- and corrosion resistance of the sintered part.
  • Different elements may also be added to the melt, prior to the atomisation process, which in the following atomisation process and/or at sintering of the component will form substances enhancing the machinability. An example of this is the formation of MnS phase in the atomised and annealed powder, and/or in the sintered component.
  • a problem when compacting alloyed iron-based powders is that such powders are harder and have less compressibility.
  • premixed powder or diffusion bonded compositions instead of corresponding pre-alloyed compositions, the compressibility can to a certain extent be enhanced.
  • a drawback with premixed powder compositions is however that segregation of the finer alloying elements within the coarser iron powder bulk may occur. Segregation can be reduced by using so called bonded compositions, i.e. the finer alloying elements are bonded to the surface of the coarser iron powders by a binder, or the finer alloying elements are bonded to the surface of the iron powder through applying a thermal diffusion binding process.
  • Pressed and sintered components made from inhomogeneous iron based powder compositions such as premixed compositions, bonded compositions or diffusion alloyed compositions will all exhibit an inhomogeneous micro structure which for certain applications is less desirable.
  • the risk of obtain inhomogeneous density distribution, leading to non uniform shrinkage during sintering, may be higher compared to using a pre-alloyed powder.
  • MIM Metal Injection Moulding
  • D 50 is a technique where very fine metal powders, typically having a value D 50 below 10 ⁇ m, are used (D 50 ; 50 % by weight of the particles have a diameter less than D 50 , 50 % by weight have a diameter above D 50 ).
  • the powder is mixed with high amounts of organic binders and lubricants in order to form a paste suitable to be injected in a die.
  • the injected component is released from the die and is subsequently subjected to a de-binding process for removing the organic material followed by a sintering process.
  • Small complex shaped components having low porosity can be produced by this method.
  • a drawback is, however, a low production speed.
  • the use of costly organic material also contributes to a relatively high production cost.
  • the patent application DE10 2009 004 881 A1 describes the production of a turbocharger component by this method.
  • US patent application US2008/0202651 discloses a method for manufacturing a high density iron- based compact including the steps of mixing an iron- base powder with graphite, subjecting the mixture to precompaction and thereafter to presintering at a temperature of 1000-1300°C, the obtained presintered body having a content of C between 0.10-0.50%, oxygen 0.3 % or less, nitrogen 0.010 or less, the density being 7.2 g/cm 3 or above.- The presintered being thereafter subjected to high velocity compaction and optionally to resinteritng or heat treatment.
  • the composition must also flow fast enough during the filling stage to obtain an economical production speed.
  • Apparent density, flowability and flow rate are commonly referred to as powder properties.
  • Various methods for agglomeration of fine powders to coarser agglomerates having sufficient powder properties and still enhancing shrinkage during sintering have been suggested in order to overcome the above mentioned problems.
  • JP3527337B2 describes a method for producing agglomerated spray dried powder from fine metal powder or pre alloyed powder.
  • Components for turbocharger such as unison or nozzle rings and sliding nozzles, usually contain hard phases in order to withstand wear at elevated temperature. Such hard phases may be carbides or nitrides. Such components also contain various alloying elements in order to provide enough strength at elevated temperatures above 700°C. The presence of hard phases in combination with alloying elements has however normally a negative influence of compressibility of the iron-based powder composition and of the machinability of the sintered components. Further, in order to reach a low porosity, high sintered density, of the sintered component such components have to undergo a high degree of shrinkage during sintering, increasing the risk of obtaining components having an unacceptable variation in dimensions, both within as well as between components produced.
  • the object of the present invention is to eliminate or at least to minimize the problems described above. This is achieved through a method of producing a sintered component by uniaxial compaction according to claim 1 and through a sintered component according to claim 9.
  • the stainless steel powder is preferably produced by water or gas atomisation of a melt containing iron and alloying elements.
  • the stainless steel powder is preferably austenitic.
  • the powder may also be produced by mixing alloying elements with an iron-or iron- based powder.
  • the particle size of the atomised stainless steel powder having in this context a coarse particle size distribution which normally in the technical field is referred to as a "100 mesh powder"(particle size below 100 mesh, 150 ⁇ m) or coarser.
  • Such particle atomised stainless steel powder may have a mean particle size between 50-100 ⁇ m, 10-50 % of the particles being less than ⁇ m and less than 5 % above 212 ⁇ m.
  • the particle size distribution may be coarser such that less than 10 % being below 45 ⁇ m and at least 40, preferably at least 60 % by weight being above 106 ⁇ m or 212 ⁇ m.
  • the amount of Cr is between 12-30% of the stainless steel powder. Cr contributes to corrosion resistance in various atmospheres such as a sulphur containing atmosphere at elevated temperatures. Cr also contributes to high temperature creep- and rupture strength. Cr may also form carbides or nitrides which may be beneficial for wear resistance. A minimum of 12 % Cr is needed in order to obtain sufficient corrosion resistance, above 30 % Cr the compressibility of the stainless steel powder will be negatively influenced.
  • Ni contributes to the stability of austenite which enhance the strength of the component at high temperatures. Ni improves also the toughness and ductility and increases the resistance of the component against oxidisation, carburization, nitriding, thermal fatigue and strong acids.
  • the upper limit for Ni is 25% in order not to negatively influence the compressibility of the powder.
  • Mo contributes to improved pitting resistance and enhances high temperature mechanical properties. Mo may also act as a carbide forming element. The content of Mo is between 0-5%. Contents above 5% is not regarded as cost effective.
  • One or more of these elements amy be present at a content of 0-5%. These elements are carbide and nitride forming elements thus contributing to wear resistance. As in the case of Mo, content above 5% is not regarded as being cost effective.
  • the content of C in the stainless steel powder shall be less than 0.1 % in order not to deteriorate the compressibility as the presence of C has a great impact on the hardness of the powder.
  • Si may be present up to 3%. Si may decrease the melting temperature of the melt prior to atomisation thus facilitating the atomisation process. Si may also act as desoxidising agent in the melt and during atomisation. A content above 3 % will negatively influence the compressibility.
  • Mn may contribute to enhanced strength of the sintered component and may be present at a content up to 2 %. As Mn is easily oxidized a content above 2 % will give to high content of oxide inclusions in the steel powder. Mn may also be present in the form of MnS which provides machinability enhancing properties to the sintered component.
  • the stainless steel powder further comprises inevitable impurities and being balanced with iron.
  • the steel powder composition is obtained by mixing the steel powder with graphite in an amount of 0.1-3%. In order to for sufficient amount of carbides during sintering the minimum amount of graphite is 0.1%. A content of graphite above 3% is relevant in relation to the amount of carbide forming elements in the stainless steel powder.
  • One or more conventional lubricants may be added to the stainless steel powder composition at an amount of up to 1.5%by weight of the composition.
  • a copper or copper containing powder may be added to the stainless steel powder composition at a content of 2%.
  • Cu will during sintering form a liquid phase thus facilitate sintering. Additions above 2% Cu will however have a negative influence of the dimensional stability of the component.
  • a phosphorous containing powder, such as Fe 3 P may be added up to 2%.
  • P has the same effect as Cu.
  • One or more conventional machinability enhancing agents may be added in an amount of up to 1%. Above a content of 1% the compressibility of the composition will be negatively influenced.
  • the machinability enhancing agent may be chosen from the group of MnS, CaF 2 , MoS 2 , hexagonal BN, bentonite or mica such as muscovite.
  • MnS may be formed from in the melt present Mn and S.
  • the process for producing the heat resistant stainless sintered steel part includes the following steps;
  • the compaction and recompaction may be performed in a conventional unaxial powder compaction equipment the recompaction may be performed in a preferred embodiment according to high velocity compaction (HVC) with the aid of a compaction machine, example of such machine is for example described in US patent 6,202,757 .
  • HVC high velocity compaction
  • Embodiments of the present invention disclosed herein provide compacted and sintered components produced from the above mentioned iron-based powder composition.
  • Such components may be a unison or nozzle ring or a sliding nozzle to be used in a turbocharger.
  • Components such as these are used in environments that require good resistance to wear and corrosion at elevated temperature, the microstructure of the component should therefore be mainly austenitic.
  • the content of machinability enhancing agents, such as MnS, in the sintered component is preferably 0.1-1, more preferably 0.1-0.6 % by weight.
  • MnS as a machinability enhancing agent
  • the mean value of the size of the MnS phase is preferably below 4 ⁇ m. The size of a MnS phase being determined by measuring its longest extension.
  • the component may further include carbides and/or nitrides in order to enhance mechanical properties such as strength, hardness wear and corrosion resistance.
  • Carbon and nitrogen can be provided to the composition, and/or through the atmosphere during sintering and/or heat treatment.
  • the size of the carbides and/or nitrides have a mean value below 3 ⁇ m The size of a carbide/nitride grain being determined by measuring the longest extension of the grain.
  • the upper limit for the density of the sintered component is believed to be about 7.7 g/cm 3 .
  • the sintered component is also characterised by its pore structure manifested in the presence of coalesced rounded small pores along the former particle boundaries and no presence of elongated pores.
  • the mean value of the size of the pores being less than 3 ⁇ m, preferably less than 2 ⁇ m.
  • the size of the pores measured as its longest extension.
  • the pore structure i.e. small spherical pores will enhance mechanical properties such as tensile and fatigue strength.
  • the chemical composition of the sintered component is essentially the same as the chemical composition of austenitic stainless steel powder used by having a higher C content as added graphite to the powder composition will diffusion into the matrix during the presintering enabling carbide formation.
  • an austenitic stainless steel sintered component according to the present invention may be characterised by having a content of;
  • the stainless steel powder was mixed with 0.5% A- wax and 0.55 graphite UF-4.
  • the obtained powder composition was compacted according to HVC in a HYP 35-5062 high velocity compaction machine available from Hydropulsor AB, Sweden, at 90 mm stroke length into rings having dimensions ⁇ 50/30* 10 mm to a density of 6,89 g/cm 3 ..
  • the obtained rings were thereafter soft annealed at 750°C in an atmosphere of DA (dissociated ammonia) having a dew point of -40°C for 20 minutes.
  • DA dissociated ammonia
  • the obtained components were further subjected to sintering in 90/10 at a temperature of 1280°C for 30 minutes.
  • the density obtained was determined to 7.33 g/cm 3 .
  • Figure 1 shows the presences of small round pores along the particle boundaries, the size of the pores being less than 3 ⁇ m.
  • Figure 2 shows the shape of present carbides, the size being substantially less than 4 ⁇ m.
  • MnS Manganese and sulphur present in the pre- alloyed stainless steel melt to be atomized, thus MnS is formed during the coarse of production of the stainless steel powder.
  • a pre- alloyed stainless steel powder having chemical composition according to table 3 below was used.
  • Table 4 shows the particle size distribution of the powder.
  • Table 3 chemical composition of stainless steel powder used in example 2 Element [% by weight] Cr 20.7 Ni 13.1 Si 2.5 Mn 0.98 Mo 0.03 Cu 0.02 w 0.09 Co 0.06 V 0.14 c 0.10 s 0.23 P 0.02 O 0.28 N 0.042 Fe balance Table 2; particle size distribution of stainless steel powder used in example 1 Sieve size [ ⁇ m] [% by weight on sieve] 212 0.5 180 4.2 150 7.4 106 16.7 75 19.6 63 10.4 45 13.7 ⁇ 45 27.5
  • the stainless steel powder was mixed with 0.5% A- wax and 0.55 graphite UF-4.
  • the obtained powder composition was compacted according to example 1 into rings having dimensions ⁇ 50/30*10 mm to a density of 6,58g/cm 3 .
  • the obtained rings were thereafter soft annealed at 750°C in an atmosphere of DA having a dew point of -40°C for 20 minutes.
  • HVC compaction After soft annealing the components were subjected HVC compaction according to example 1. Prior to compaction the die was painted with DWL Zn- stearate suspended in acetone. The obtained density was 6.88g/cm 3 .
  • the obtained components were further subjected to sintering in 90/10 at a temperature of 1280°C for 30 minutes.
  • the density was 7.17 gcm 3 .
  • the obtained finished density was lower compared to example 1.
  • Figure 3 shows the presences of small round pores along the particle boundaries, the size of the pores being less than 3 ⁇ m.
  • Figure 4 shows the shape of present carbides, the size being substantially less than 4 ⁇ m.
  • example 3 the same stainless steel powder as used in example 1 was used.
  • the stainless steel powder was mixed with 0.5% A- wax and 0.55 graphite UF-4. and 0.5% of MnS having a mean particle size of less 5 ⁇ m.
  • the obtained powder composition was compacted according to example 1 into rings having dimensions ⁇ 50/30*10 mm to a density of 6.84 g/cm 3 .
  • the obtained rings were thereafter soft annealed at 750°C in an atmosphere of DA having a dew point of -40°C for 20 minutes.
  • the components were subjected HVC compaction in a die. Prior to compaction the die was painted with DWL Zn- stearate suspended in acetone. The obtained density was 7.23 g/cm 3 .
  • the obtained components were further subjected to sintering in 90/10 at a temperature of 1280°C for 30 minutes.
  • the obtained sintered density was 7.33 g/cm 3 .
  • Figure 5 shows the presences of small round pores along the particle boundaries, the size of the pores being less than 3 ⁇ m.
  • Machinablity was tested on components made according to the three examples, as reference material a similar full dense cast material was used.
  • the drills used were Drill Dornier ⁇ 3.5 mm, A002.
  • the feed rate 0.06 mm/revolution.
  • the number of holes drilled before the drills were worn out at various cutting speeds were noted as a measurement of the machinabilty.
  • Table 5 shows the results; Table 5, results from machinabilty testing Cutting speed [meter/minute] Component according to Ex 1 [no of holes] Component according to Ex 2 [no of holes] Component according to Ex 3 [no of holes] Reference, cast material [no of holes] 10 61 31 20 210 121 15 30 24 8 15 12 40 7 7
  • Table 5 shows that sintered parts made according to the invention exhibit improved machinability properties even if no machinability agent is added, example 1, as compared to the reference material. Presence of machinability enhancing agent further improves the machinability, example 2 and 3. Best result is obtained when the machniablity agent, MnS, is present as small inclusions in the matrix, the size of the MnS phase being less than 4 ⁇ m, example 2.

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
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EP11162124A 2011-04-12 2011-04-12 Sintermetallurgiezusammensetzung und gesinterte Komponente Withdrawn EP2511031A1 (de)

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EP11162124A EP2511031A1 (de) 2011-04-12 2011-04-12 Sintermetallurgiezusammensetzung und gesinterte Komponente
PCT/EP2012/056544 WO2012140057A1 (en) 2011-04-12 2012-04-11 A powder metallurgical composition and sintered component

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Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2772558A3 (de) * 2013-03-01 2014-10-22 Hitachi Chemical Company, Ltd. Gesinterte Legierung und Herstellungsverfahren dafür
WO2015091366A1 (en) * 2013-12-20 2015-06-25 Höganäs Ab (Publ) A method for producing a sintered component and a sintered component
CN108103499A (zh) * 2017-12-22 2018-06-01 北京机科国创轻量化科学研究院有限公司 一种用于超高速激光熔覆的颗粒增强铁基金属粉末
KR20190092493A (ko) * 2016-12-07 2019-08-07 회가내스 아베 (피유비엘) 듀플렉스 소결된 스테인리스 강을 제조하기 위한 스테인리스 강 분말
CN110300635A (zh) * 2016-12-16 2019-10-01 天纳克有限责任公司 测温冶金材料
EP3822379A4 (de) * 2018-07-11 2021-08-25 Showa Denko Materials Co., Ltd. Sinterlegierung und verfahren zur herstellung davon

Families Citing this family (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2584832C2 (ru) * 2014-09-11 2016-05-20 Павел Аркадьевич Киселёв Спечённые коррозионностойкие материалы на основе железа
JP6920877B2 (ja) * 2017-04-27 2021-08-18 株式会社ダイヤメット 高温耐摩耗性、耐塩害性に優れる耐熱焼結材及びその製造方法

Citations (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2411073A (en) * 1944-08-16 1946-11-12 Isthmian Metals Inc Making products of iron or iron alloys
US3980444A (en) * 1975-01-22 1976-09-14 Allegheny Ludlum Industries, Inc. Sintered liquid phase stainless steel
US4985309A (en) * 1987-08-01 1991-01-15 Kawasaki Steel Corporation Alloyed steel powder for powder metallurgy
US6202757B1 (en) 1995-06-21 2001-03-20 Hydropulsor Ab Impact machine
US6503443B1 (en) 1999-04-16 2003-01-07 Unisia Jecs Corporation Metallic powder molding material and its re-compression molded body and sintered body obtained from the re-compression molded body and production methods thereof
US20030230165A1 (en) * 2002-06-14 2003-12-18 Anders Bergkvist Warm compaction of steel powders
JP3527337B2 (ja) 1995-10-06 2004-05-17 住友特殊金属株式会社 金属又は合金物品の製造方法
US20080202651A1 (en) 2004-11-25 2008-08-28 Jfe Steel Corporation Method For Manufacturing High-Density Iron-Based Compacted Body and High-Density Iron-Based Sintered Body
DE102009004881A1 (de) 2009-01-16 2010-07-29 Bosch Mahle Turbo Systems Gmbh & Co. Kg Ladeeinrichtung
JP2010215951A (ja) * 2009-03-16 2010-09-30 Hitachi Powdered Metals Co Ltd 焼結複合摺動部品およびその製造方法

Patent Citations (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2411073A (en) * 1944-08-16 1946-11-12 Isthmian Metals Inc Making products of iron or iron alloys
US3980444A (en) * 1975-01-22 1976-09-14 Allegheny Ludlum Industries, Inc. Sintered liquid phase stainless steel
US4985309A (en) * 1987-08-01 1991-01-15 Kawasaki Steel Corporation Alloyed steel powder for powder metallurgy
US6202757B1 (en) 1995-06-21 2001-03-20 Hydropulsor Ab Impact machine
JP3527337B2 (ja) 1995-10-06 2004-05-17 住友特殊金属株式会社 金属又は合金物品の製造方法
US6503443B1 (en) 1999-04-16 2003-01-07 Unisia Jecs Corporation Metallic powder molding material and its re-compression molded body and sintered body obtained from the re-compression molded body and production methods thereof
US20030230165A1 (en) * 2002-06-14 2003-12-18 Anders Bergkvist Warm compaction of steel powders
US20080202651A1 (en) 2004-11-25 2008-08-28 Jfe Steel Corporation Method For Manufacturing High-Density Iron-Based Compacted Body and High-Density Iron-Based Sintered Body
DE102009004881A1 (de) 2009-01-16 2010-07-29 Bosch Mahle Turbo Systems Gmbh & Co. Kg Ladeeinrichtung
JP2010215951A (ja) * 2009-03-16 2010-09-30 Hitachi Powdered Metals Co Ltd 焼結複合摺動部品およびその製造方法

Cited By (16)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2772558A3 (de) * 2013-03-01 2014-10-22 Hitachi Chemical Company, Ltd. Gesinterte Legierung und Herstellungsverfahren dafür
US9982562B2 (en) 2013-03-01 2018-05-29 Hitachi Chemical Company, Ltd. Sintered alloy and manufacturing method thereof
US9982563B2 (en) 2013-03-01 2018-05-29 Hitachi Chemical Company, Ltd. Sintered alloy and manufacturing method thereof
EP3378960A1 (de) * 2013-03-01 2018-09-26 Hitachi Chemical Company, Ltd. Gesinterte legierung
WO2015091366A1 (en) * 2013-12-20 2015-06-25 Höganäs Ab (Publ) A method for producing a sintered component and a sintered component
CN105829560A (zh) * 2013-12-20 2016-08-03 霍加纳斯股份有限公司 制造经烧结组件的方法以及经烧结组件
JP2017504717A (ja) * 2013-12-20 2017-02-09 ホガナス アクチボラグ （パブル） 焼結部材の製造方法及び焼結部材
US11554416B2 (en) 2013-12-20 2023-01-17 Höganäs Ab (Publ) Method for producing a sintered component and a sintered component
US11179778B2 (en) 2013-12-20 2021-11-23 Höganäs Ab (Publ) Method for producing a sintered component and a sintered component
TWI655981B (zh) * 2013-12-20 2019-04-11 瑞典商好根那公司 製造經燒結之組件的方法及經燒結之組件
CN105829560B (zh) * 2013-12-20 2019-09-27 霍加纳斯股份有限公司 制造经烧结组件的方法以及经烧结组件
KR20190092493A (ko) * 2016-12-07 2019-08-07 회가내스 아베 (피유비엘) 듀플렉스 소결된 스테인리스 강을 제조하기 위한 스테인리스 강 분말
CN110300635A (zh) * 2016-12-16 2019-10-01 天纳克有限责任公司 测温冶金材料
CN108103499B (zh) * 2017-12-22 2018-11-27 北京机科国创轻量化科学研究院有限公司 一种用于超高速激光熔覆的颗粒增强铁基金属粉末
CN108103499A (zh) * 2017-12-22 2018-06-01 北京机科国创轻量化科学研究院有限公司 一种用于超高速激光熔覆的颗粒增强铁基金属粉末
EP3822379A4 (de) * 2018-07-11 2021-08-25 Showa Denko Materials Co., Ltd. Sinterlegierung und verfahren zur herstellung davon

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