EP2207907B1 - Metallurgical powder composition and method of production - Google Patents

Metallurgical powder composition and method of production Download PDF

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Publication number
EP2207907B1
EP2207907B1 EP08804654.5A EP08804654A EP2207907B1 EP 2207907 B1 EP2207907 B1 EP 2207907B1 EP 08804654 A EP08804654 A EP 08804654A EP 2207907 B1 EP2207907 B1 EP 2207907B1
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EP
European Patent Office
Prior art keywords
iron
weight
based powder
powder
chromium carbides
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Not-in-force
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EP08804654.5A
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German (de)
English (en)
French (fr)
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EP2207907A1 (en
Inventor
Ola Bergman
Paul Dudfield Nurthen
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Hoganas AB
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Hoganas AB
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Priority to PL08804654T priority Critical patent/PL2207907T3/pl
Publication of EP2207907A1 publication Critical patent/EP2207907A1/en
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Publication of EP2207907B1 publication Critical patent/EP2207907B1/en
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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
    • C22C33/0207—Using a mixture of prealloyed powders or a master alloy
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
    • F01L3/00—Lift-valve, i.e. cut-off apparatus with closure members having at least a component of their opening and closing motion perpendicular to the closing faces; Parts or accessories thereof
    • F01L3/02—Selecting particular materials for valve-members or valve-seats; Valve-members or valve-seats composed of two or more materials
    • 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
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
    • F01L2301/00—Using particular materials
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
    • F01L2301/00—Using particular materials
    • F01L2301/02—Using ceramic materials
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
    • F01L2303/00—Manufacturing of components used in valve arrangements
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
    • F01L2820/00—Details on specific features characterising valve gear arrangements
    • F01L2820/01—Absolute values

Definitions

  • the present invention relates to an iron-based powder. Especially the invention concerns a powder suitable for the production of wear-resistant products such as valve seat inserts (VSI) as well as a component made from the powder.
  • VSI valve seat inserts
  • the manufacture of products having high wear-resistance may be based on e.g. powders, such as iron or iron-based powders, including carbon in the form of carbides.
  • Carbides are very hard and have high melting points, characteristics which give them a high wear resistance in many applications. This wear resistance often makes carbides desirable as components in steels, e.g. high speed steels (HSS) that require a high wear resistance, such as steels for drills, lathes, valve seat inserts and the likes.
  • HSS high speed steels
  • a VSI in a combustion engine is a ring that is inserted where the valve comes in contact with the cylinder head during operation.
  • the VSI is used to limit the wear, caused by the valve, on the cylinder head. This is done by using a material in the VSI that can resist wear better than the cylinder head material, without wearing on the valve.
  • the materials used for VSI are cast materials or more commonly pressed and sintered PM materials.
  • the method of fabricating a PM valve seat insert starts with preparation of a mix which includes all ingredients needed in the final component.
  • the powder mix most commonly includes an iron or low alloyed powder serving as matrix in the final component, elemental alloying elements such as C, Cu, Ni, Co etc which should to a lower or higher extent diffuse into the matrix material and enhance strength and hardness.
  • Further hard phase materials containing carbides and similar phases can be added to increase the wear resistance of the alloy. It is also common to have machinability enhancers added to decrease tool wear when machining the finished product, as well as solid lubricants in order to assist the lubrication during service in the engine.
  • evaporative lubricants are added to assist compaction and ejection of the compacted component.
  • a known VSI material produced by Powder Metallurgy, is based on high speed steel powder as carbide containing matrix material. All powders used normally have a particle size of less than 180 ⁇ m. The average particle size of the mix is usually between 50 to 100 ⁇ m to allow the mix to flow and facilitate production.
  • the alloying and lubricant additives are in many cases finer in particle size compared to the matrix powder to improve distribution of alloying elements in the powder mix and finished component.
  • the powder mix is then fed into a tool cavity with the shape of a VSI ring.
  • An axial pressure between 400-900 MPa is applied resulting in a near net shape metallic VSI component having a density between 6.4-7.3 g/cm 3 .
  • dual compaction is used to decrease the use of expensive alloying elements.
  • two different powder mixes are used. One more expensive with excellent wear properties creating the wear surface of VSI facing the valve and one less costly to give the desired height of the component.
  • the individual grains are only loosely bonded through cold welding, and a subsequent sintering operation is required to allow the individual particles to diffuse together and to distribute alloying elements.
  • Sintering is usually performed at temperatures between 1120°C and 1150°C but temperatures up to 1300°C can be used, in a reducing atmosphere usually based on Nitrogen and Hydrogen.
  • copper can be infiltrated in the pores of the component to increase hardness and strength as well as improve heat conductivity and wear properties.
  • subsequent heat treatments are performed to reach final properties.
  • the final machining is in many cases done after VSI is mounted in the cylinder head. The final machining is done in order to give the VSI and inverted valve profile and to have small dimensional variations.
  • W, V, Mo, Ti and Nb are strong carbide forming elements which make these elements especially interesting for the production of wear resistant products.
  • Cr is another carbide forming element.
  • Most of these conventional carbide forming metals are, however, expensive and result in an inconveniently high priced product.
  • chromium is a much cheaper and more readily available carbide forming metal than other such metals used in conventional powders and hard phases with high wear resistance, it would be desirable to be able to use chromium as principal carbide forming metal. In that way the powder, and thus the compacted product, can be more inexpensively produced.
  • the carbides of regular high speed steels are usually quite small, but in accordance with the present invention it has now unexpectedly been shown that powders having equally advantageous wear resistance, for e.g. valve seat applications, may be obtained with chromium as the principal carbide forming metal, provided that a sufficient amount of large carbides exists, supported by a minor amount of finer and harder carbides.
  • An objective of the present invention is thus to provide an inexpensive iron-based powder for the manufacture of powder metallurgical products having a high wear resistance.
  • an annealed pre-alloyed water atomised iron-based powder comprising from 10 to below 18 % by weight of Cr, 0.5-5% by weight of each of at least one of Mo, W, V and Nb, 0.5-2%, preferably 0.7-2% and most preferably 1-2% by weight of C and balance being Fe, wherein the iron-based powder has a matrix comprising less than 10% by weight of Cr.
  • the iron-based powder may optionally include 0-2% silicon and mandatory comprises large chromium carbides and finer and harder chromium carbides. The large chromium carbides having an average size of 8-45 ⁇ m and smaller and harder chromium carbides having an average size less than 8 ⁇ m.
  • this new powder which achieves the above objectives may be obtained through a method of producing an iron-based powder as defined in present claim 1 comprising subjecting an iron-based melt including 10- below 18% by weight of Cr, 0.5-5% by weight of each of at least one of Mo, W, V and Nb and 0.5-2%, preferably 0.7-2% most and preferably 1-2% by weight of C and balance being Fe to water atomisation in order to obtain iron-based powder particles, and annealing the powder particles at a temperature, and for a period of time, sufficient for obtaining the desired carbides within the particles. It has been found that temperatures in the range of 900-1100°C and annealing times in the range of 15-72 hours are sufficient for obtaining the desired carbides within the particles.
  • the pre-alloyed powder of the invention contains chromium, 10- below 18% by weight, at least one of molybdenum, tungsten, vanadium and niobium, 0.5-5% by weight of each, and carbon, 0.5-2%, preferably 0.7-2% and most preferably 1-2% by weight, optionally 0-2% silicon the balance being iron, and inevitable impurities.
  • the pre-alloyed powder preferably has an average particle size in the range of 40-100 ⁇ m, preferably of about 80 ⁇ m.
  • the pre-alloyed powder comprises 12-17% by weight of Cr, such as 15-17% by weight of Cr, e.g. 16% by weight of Cr.
  • the pre-alloyed powder comprises 12- below 18% by weight of Cr, 1-3 wt% of Mo, 1-3,5 wt% of W, 0.5-1.5 wt% of V, 0.2-1 wt% of Si, 1-2 wt% of C and balance Fe.
  • the pre-alloyed powder comprises 14-below 18 weight of Cr, 1-2 wt% of Mo, 1-2 wt% of W, 0.5-1.5 wt% of V, 0.2-1 wt% of Si, 1-2 wt% of C and balance Fe.
  • the pre-alloyed powder comprises 12-below 15 weight of Cr, 1-2 wt% of Mo, 2-3 wt% of W, 0.5-1.5 wt% of V, 0.2-1 wt% of Si, 1-2 wt% of C and balance Fe.
  • the powder may further comprise other than the above carbide types.
  • the large carbides of the inventive powder have an average size in the range of 8-45 ⁇ m, more preferably in the range of 8-30 ⁇ m, a hardness of about 1100-1300 microvickers and preferably make up 10-30% by volume of the total powder.
  • the M 7 C 3- type smaller carbides of the inventive powder are smaller and harder than the M 23 C 6- type large carbides.
  • the smaller carbides of the inventive powder have an average size below 8 ⁇ m, a hardness of about 1400-1600 microvickers and preferably make up 3-10% by volume of the total powder.
  • size defines the longest extension as measured in a microscope.
  • the pre-alloyed powder is subjected to prolonged annealing, preferably under vacuum.
  • the annealing is performed in the range of 900-1100°C, most preferably at about 1000°C, at which temperature chromium of the pre-alloyed powder reacts with carbon to form chromium carbides.
  • annealing During the annealing, new carbides are formed and grow and existing carbides continue to grow through reaction between chromium and carbon. The annealing is continued for 15-72 hours, more preferably for more than 48 hours, in order to obtain carbides of desired size. The longer the duration of the annealing, the larger the carbide grains grow. However, the annealing consumes lots of energy and might be a production flow bottle neck if it continues for a long time.
  • an average chromium carbide grain size of the large chromium carbides of about 20-30 ⁇ m may be optimal, it might, depending on priority, be more convenient from an economic point of view to terminate the annealing earlier, when the average chromium carbide grain size of the large chromium carbides is about 10 ⁇ m.
  • Very slow cooling preferably more than 12 hours, from annealing temperature is applied. Slow cooling will allow further growth of carbides, as a larger amount of carbides is thermodynamically stable at lower temperatures. Slow cooling will also assure that the matrix becomes ferritic, which is important for the compressibility of the powder.
  • Annealing the powder also has other advantages besides the growth of carbides.
  • the carbon and oxygen contents of the powder may be adjusted. It is usually desirable to keep the oxygen content low.
  • carbon is reacted with oxygen to form gaseous carbon oxide, which reduces the oxygen content of the powder. If there is not enough carbon in the pre-alloyed powder itself, for both forming carbides and reducing the oxygen content, additional carbon, in form of graphite powder, may be provided for the annealing.
  • the matrix of the resulting annealed powder has a content of dissolved chromium of less than 10% by weight of the matrix, preferably less than 9% by weight and most preferably less than 8% by weight, why the powder is not stainless.
  • the matrix composition of the powder is designed such that ferrite transforms to austenite during sintering. Thereby, the austenite can transform into martensite upon cooling after sintering. Large carbides in combination with smaller and harder carbides in a martensitic matrix will give good wear resistance of the pressed and sintered component.
  • the annealed powder of the invention may be mixed with other powder components, such as other iron-based powders, graphite, evaporative lubricants, solid lubricants, machinability enhancing agents etc, before compaction and sintering to produce a product with high wear resistance.
  • other powder components such as other iron-based powders, graphite, evaporative lubricants, solid lubricants, machinability enhancing agents etc, before compaction and sintering to produce a product with high wear resistance.
  • One may e.g. mix the inventive powder with pure iron powder and graphite powder, or with a stainless steel powder.
  • a lubricant such as a wax, stearate, metal soap or the like, which facilitates the compaction and then evaporates during sintering, may be added, as well as a solid lubricant, such as MnS, CaF 2 , MoS 2 , which reduces friction during use of the sintered product and which also may enhance the machinability of the same. Also other machinability enhancing agents may be added, as well as other conventional additives of the powder metallurgical field.
  • the obtained mix is well suited for compacting into near net shape VSI components having a chamfered inverted valve profile.
  • a melt of 16.0 wt% Cr, 1.5 wt% Mo, 1.5 wt% W, 1 wt% V, 0.5 wt% Si, 1.5 wt% C and balance Fe was water atomised to form a pre-alloyed powder.
  • the obtained powder was subsequently vacuum annealed at 1000°C for about 48 hours, the total annealing time being about 60 hours, after which the powder particles contained about 20% by volume of M 23 C 6 -type carbides of an average grain size of about 10 ⁇ m and about 5% by volume of M 7 C 3 -type carbides of an average grain size of about 3 ⁇ m in a ferritic matrix.
  • the obtained powder (hereafter referred to as OB1) was mixed with 0.5 wt% graphite and 0.75 wt% of an evaporative lubricant.
  • the mix was compacted into test bars at a pressure of 700 MPa.
  • the obtained samples were sintered in an atmosphere of 90N 2 /10H 2 at a temperature of 1120°C. After sintering the samples were subjected to cryogenic cooling in liquid nitrogen followed by tempering at 550°C.
  • the microstructure of the OB1 test material (see Figure 1 ) consists of the desired mixture of large and small carbides in a martensitic matrix.
  • the reference material has similar microstructure (see Figure 2 ) but with smaller carbides than the OB1 material.
  • the OB1 material has somewhat higher porosity than the M3/2 material, which explains why the OB1 hardness values (HV5) are lower than those for M3/2 although the OB1 microhardness is higher than that for M3/2.
  • HV5 OB1 hardness values
  • the porosity is normally eliminated by copper infiltration during sintering and such effects can therefore be neglected.
  • the hardness values of the OB1 material are comparable to those of the reference M3/2 material, which gives good indication that the materials should have comparable wear resistance.
  • maintaining hardness at elevated temperatures is important for wear resistance in VSI applications.
  • the hot hardness test results show that the OB1 material meets these requirements.
  • a melt of 14,5 wt% Cr, 1.5 wt% Mo, 2.5 wt% W, 1 wt% V, 0.5 wt% Si, 1.5 wt% C and balance Fe was water atomised to form a pre-alloyed powder.
  • the obtained powder was subsequently vacuum annealed at 1000°C for about 48 hours, the total annealing time being about 60 hours, after which the powder particles contained about 20% by volume of M 23 C 6 -type carbides of an average grain size of about 10 ⁇ m and about 5% by volume of M 7 C 3 -type carbides of an average grain size of about 3 ⁇ m in a ferritic matrix.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • General Engineering & Computer Science (AREA)
  • Powder Metallurgy (AREA)
  • Manufacture Of Metal Powder And Suspensions Thereof (AREA)
EP08804654.5A 2007-09-28 2008-09-24 Metallurgical powder composition and method of production Not-in-force EP2207907B1 (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
PL08804654T PL2207907T3 (pl) 2007-09-28 2008-09-24 Kompozycja metalurgii proszkowej i sposób wytwarzania

Applications Claiming Priority (3)

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DKPA200701397 2007-09-28
US96052507P 2007-10-02 2007-10-02
PCT/EP2008/062745 WO2009040369A1 (en) 2007-09-28 2008-09-24 Metallurgical powder composition and method of production

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EP2207907A1 EP2207907A1 (en) 2010-07-21
EP2207907B1 true EP2207907B1 (en) 2017-12-06

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EP (1) EP2207907B1 (ru)
JP (1) JP5481380B2 (ru)
KR (1) KR101551453B1 (ru)
CN (1) CN101809180B (ru)
BR (1) BRPI0817619B1 (ru)
CA (1) CA2700056C (ru)
ES (1) ES2659979T3 (ru)
PL (1) PL2207907T3 (ru)
RU (1) RU2462524C2 (ru)
TW (1) TWI400341B (ru)
WO (1) WO2009040369A1 (ru)

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CN101590524B (zh) * 2009-06-23 2013-11-20 诸城市同翔机械有限公司 用于高强度粉末冶金气门导管材料的配制原料
WO2013101561A1 (en) 2011-12-30 2013-07-04 Scoperta, Inc. Coating compositions
US10702924B2 (en) 2012-01-05 2020-07-07 Höganäs Ab (Publ) Metal powder and use thereof
CN102660709A (zh) * 2012-04-24 2012-09-12 邓湘凌 高强度耐磨合金及其制作方法
WO2015091366A1 (en) * 2013-12-20 2015-06-25 Höganäs Ab (Publ) A method for producing a sintered component and a sintered component
DE102015213706A1 (de) 2015-07-21 2017-01-26 Mahle International Gmbh Tribologisches System, umfassend einen Ventilsitzring und ein Ventil
CA2997367C (en) 2015-09-04 2023-10-03 Scoperta, Inc. Chromium free and low-chromium wear resistant alloys
CN110418688B (zh) * 2017-03-14 2022-04-05 Vbn组件有限公司 高碳含量钴基合金
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US20210262050A1 (en) 2018-08-31 2021-08-26 Höganäs Ab (Publ) Modified high speed steel particle, powder metallurgy method using the same, and sintered part obtained therefrom
US11939646B2 (en) 2018-10-26 2024-03-26 Oerlikon Metco (Us) Inc. Corrosion and wear resistant nickel based alloys
CN113649583A (zh) * 2021-08-09 2021-11-16 天工爱和特钢有限公司 一种高速钢粉末冶金制品的制备方法

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TW200925295A (en) 2009-06-16
KR101551453B1 (ko) 2015-09-08
ES2659979T3 (es) 2018-03-20
CA2700056C (en) 2016-08-16
CN101809180A (zh) 2010-08-18
JP2010540772A (ja) 2010-12-24
BRPI0817619B1 (pt) 2018-04-24
PL2207907T3 (pl) 2018-04-30
RU2010116699A (ru) 2011-11-10
CA2700056A1 (en) 2009-04-02
JP5481380B2 (ja) 2014-04-23
CN101809180B (zh) 2013-04-03
BRPI0817619A2 (pt) 2015-03-31
EP2207907A1 (en) 2010-07-21
RU2462524C2 (ru) 2012-09-27
TWI400341B (zh) 2013-07-01
KR20100075571A (ko) 2010-07-02
WO2009040369A1 (en) 2009-04-02

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