EP1370704B1 - Process of production of a sintered ferrous material containing copper - Google Patents

Process of production of a sintered ferrous material containing copper Download PDF

Info

Publication number
EP1370704B1
EP1370704B1 EP02715503A EP02715503A EP1370704B1 EP 1370704 B1 EP1370704 B1 EP 1370704B1 EP 02715503 A EP02715503 A EP 02715503A EP 02715503 A EP02715503 A EP 02715503A EP 1370704 B1 EP1370704 B1 EP 1370704B1
Authority
EP
European Patent Office
Prior art keywords
powder
copper
iron
process according
steel
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.)
Expired - Lifetime
Application number
EP02715503A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP1370704A1 (en
Inventor
Paritosh Maulik
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.)
Federal Mogul Coventry Ltd
Original Assignee
Federal Mogul Sintered Products Ltd
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Priority claimed from GB0101770A external-priority patent/GB0101770D0/en
Priority claimed from GB0120401A external-priority patent/GB0120401D0/en
Application filed by Federal Mogul Sintered Products Ltd filed Critical Federal Mogul Sintered Products Ltd
Publication of EP1370704A1 publication Critical patent/EP1370704A1/en
Application granted granted Critical
Publication of EP1370704B1 publication Critical patent/EP1370704B1/en
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Images

Classifications

    • 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
    • B22F3/10—Sintering only
    • 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%

Definitions

  • the present invention relates to the production of sintered ferrous materials, articles made therefrom particularly, ferrous materials containing copper.
  • the powder metallurgy route enables the design of metallic materials which it is not possible to make by conventional casting and ingot working processes. It is known to infiltrate sintered ferrous powder metallurgical products with metals having lower melting points such as lead and copper, for example. Lead is used to improve machinability of sintered ferrous materials whilst copper also has this effect but also has other desirable properties which it confers on the sintered material. Lead is nowadays avoided due to its harmful environmental properties. Copper improves machinability and also improves the thermal conductivity of the sintered article.
  • Copper infiltrated products are used extensively in the automotive industry for applications such as valve seat inserts in the cylinder heads of internal combustion engines, for example. Such products have to perform under very arduous conditions including repeated impact loading, marginal lubrication, elevated service temperatures and hot corrosive gases. Properties to withstand these conditions are achieved by the suitable design of the ferrous matrix system. Such ferrous matrices are often highly alloyed which adversely affects machinability. Machinability is important to an engine builder in a production context as it affects productivity. Copper infiltration provides improved machinability whilst the copper itself provides improved thermal conductivity which has the effect of lowering operating service temperatures which helps to retain mechanical properties.
  • the infiltration process is effected by stacking a copper alloy compact in contact with the ferrous component and passing the stacked assembly of the two items through a sintering furnace at a sintering temperature in the region of about 1100°C under an inert or reducing gaseous atmosphere thus effecting sintering and infiltration simultaneously.
  • the copper alloy compact melts and the molten alloy infiltrates and fills the pores of the ferrous component by capillary action. Only interconnected pores can be filled in this manner, isolated or otherwise unconnected porosity cannot be so filled.
  • the composition of the copper alloy compact is so chosen that it is compatible with the ferrous material and undesirable reactions or erosion thereof is avoided as far as possible.
  • the weight of the copper alloy compact is chosen so as to be able to fill the majority of the pores, however, as noted above there is inevitably some residual porosity.
  • the copper alloy compact is stacked with a pre-sintered ferrous component and the two passed through a sintering furnace to effect infiltration.
  • the infiltration process is an expensive process owing to the extra process steps involved.
  • the process requires the additional steps of: making a separate copper alloy powder mixture; pressing suitable compacts of the correct weight from the powder mixture; stacking the compacts with the ferrous articles themselves prior to passing through the sintering furnace; and, barrelling the sintered and infiltrated articles after cooling to remove the powdery deposit which inevitably forms on the articles during the sintering process.
  • the level of copper content generally lies in the range from. 15 to 25 weight%.
  • Such relatively small additions of copper to non-infiltrated ferrous materials assist the sintering process due to the liquid copper phase being present.
  • components such as valve seat inserts for engines having the most arduous service environment were made entirely from highly alloyed steels such as M3/2 class steels for example.
  • Such steels contain relatively high quantities of chromium, tungsten, molybdenum, vanadium and the like. Whilst components made from such materials have excellent performance and long service lives, they are inherently expensive to make and process. They are expensive to make firstly because of the high intrinsic material cost and secondly expensive to process because of the difficulty in machining components having high contents of hard carbide in the microstructure thereof.
  • a disadvantage in terms of performance and longevity of life of these newer materials such as may be exemplified in GB-A-2 188 062 for example is the retention in the cores of the iron grains, formed by the sintering together of the original compacted iron powder particles in the powder mixture, of soft ferrite phase which can deleteriously affect the wear and strength. properties thereof.
  • Such materials may initially comprise mixtures of about 50% of the highly alloyed M3/2 material, for example, and about 50% of pure iron powder and minor additions of carbon, die lubricating waxes and the like.
  • the iron grains have ferrite cores with only some diffusion of chromium, from the M3/2 regions, into the surface regions of the iron grains, where martensite may be formed, after sintering. This structure still applies even when the material is infiltrated or when up to about 5 weight% of elemental copper has been added to the powder mixture.
  • a process for the production of copper-containing martensitic steel is known from CH-275201.
  • the copper content is primarily intended to enhance the thermal conductivity of articles produced, however, other important benefits are also provided to articles made by the method of the present invention. Below 12 weight% copper the required enhancement in thermal conductivity is not achieved whilst above 26 weight% "bleeding" of molten copper from the material during sintering is a problem.
  • the copper content may lie in the range from 15 to 20 weight%.
  • the iron powder indivisibly associated with copper is effectively a pre-alloyed powder in that the individual powder particles comprise both iron and copper and consequently significant segregation between the iron and copper is not possible.
  • the iron and copper powder particles may be selected from two basic types of powder stock: a pre-alloyed iron-copper powder; or, a diffusion bonded iron-copper powder.
  • the pre-alloyed iron-copper powder may be produced by known techniques of melting the constituent materials together and then atomising the molten melt by water or gas, for example, to produce the required pre-alloyed powder.
  • the diffusion bonded iron-copper material is produced by making a mixture of elemental iron and copper powders, for example, and passing the mixture, uncompacted, through a furnace such that diffusion between the particles occurs so as to bond them together.
  • the "cake” so formed is given a light crushing operation to break it up into particles comprising both iron and copper adhered to each other. Such a process causes diffusion of some copper into the outer regions of each iron particle.
  • the method of the present invention obviates several of the process steps of prior art processes in that a separate copper alloy powder mixture and consequent compacts do not need to be made, they do not need to be stacked with the ferrous material compacts and the final sintered articles do not need to be treated to remove the adherent deposit thereon as with prior art infiltration processes.
  • a particular advantage conferred by the method of the present invention relates to the processing of those ferrous materials which comprise mixtures of an alloyed steel powder and a low-alloy iron or substantially pure iron powder. It is known to use such mixtures with additions of carbon powder, for example, and to process them by compaction, sintering and post-sintering thermal treatment into articles such as valve seat inserts for internal combustion engines, for example.
  • Such prior art materials may or may not be infiltrated with a copper alloy by one of the conventional processes described above.
  • Such materials are exemplified by those materials and production processes described in GB-A-2 188 062 and EP-A-0 312 161, for example. These materials may comprise a proportion, e.g.
  • the alloyed steel powder usually contains chromium which under the prevailing sintering conditions of about 1100°C is one of the most mobile element atoms after carbon, in terms of rate of diffusion, of those alloying elements which promote the formation of martensite on cooling of the article following sintering. Carbon atoms are the most mobile, moving into the interstices of the iron atoms in the crystal structure. However, since chromium is of a similar atomic size and weight to iron it substitutes for iron and consequently has a similar mobility to iron under the prevailing sintering conditions.
  • chromium promotes the formation of martensite in those regions of the sintered material into which it diffuses, the martensite being formed on cooling of the material at the end of the sintering cycle.
  • Sintering is frequently effected for such articles in furnaces which have continuous moving means, such as a belt or a walking-beam type mechanism, for transporting the articles, generally supported on trays for example, through the furnace.
  • continuous moving means such as a belt or a walking-beam type mechanism
  • a first portion of the furnace raises the temperature of the articles to the sintering temperature; a second portion maintains the articles at the sintering temperature; and, a third portion allows the articles to cool from the sintering temperature to a temperature which will preclude significant oxidation of the articles on exit from the sintering furnace.
  • the articles are generally sintered under a continuous protective gas atmosphere flowing through the furnace which serves to provide either a neutral or reducing atmosphere and preclude air (oxygen) from entering the furnace.
  • the atmosphere is at substantially atmospheric pressure with only a slight positive pressure within the furnace to prevent air from entering therein.
  • the outer region of the iron grains generally comprises martensite resulting from chromium which has diffused in during the sintering operation but the core remains essentially as ferrite or pearlite or a mixture of ferrite and pearlite depending upon the added carbon level.
  • the iron-rich non-tool steel phase or grain structure consists of mainly pearlite, though there may be some ferrite, at the centre and the outer regions of the grains are a mixture of martensite/bainite. If there is any retained austenite in the sintered article it is generally transformed by cryogenic treatment after sintering.
  • valve seat insert in the combustion chamber of an internal combustion engine is ensured.
  • such treatments do not affect the presence (other than to be responsible for generating at least a proportion of the ferrite) of the ferrite phase or its inherently poor wear and mechanical properties.
  • Sintered ferrous materials made according to the process of the present invention using either pre-alloyed iron-copper or diffusion bonded iron-copper powders reveal the presence of martensite in the cores of the iron-rich grains due to the diffusion of chromium or other martensite promoting elements into the iron grains.
  • the martensite is formed during the cooling of austenite and any retained austenite is transformed by cryogenic treatment following sintering. During the cooling process from the sintering temperature some of the austenite can also transform to bainite.
  • the martensite may then be tempered to form a structure of tempered martensite which is readily machinable.
  • the previously soft ferritic/pearlitic cores of the iron grains now comprise material which is harder, stronger and more wear resistant due to the process of the present invention. It is believed that the processing used to form the pre-alloyed and diffusion bonded iron-copper material causes at least some diffusion of the copper phase into the iron constituent and the presence of the copper assists in the diffusion of chromium and other martensite promoting elements into the cores of the iron grains formed on sintering thus, enabling martensite to be formed.
  • Materials of largely identical composition except for the copper content were made by 1) the method of the present invention; 2) by the route of simultaneous sintering and infiltration; and, 3) by adding 13 weight% elemental copper powder to the initial powder mixture and sintering (i.e. without infiltration and without the addition of pre-alloyed iron-copper powder).
  • Materials made according to the method of the present invention may also receive post-sintering thermal treatments such as cryogenic treatment at -120°C or below to convert any residual austenite phase to martensite, followed by tempering to make the martensite softer, more dimensionally stable and make it amenable to machining.
  • post-sintering thermal treatments such as cryogenic treatment at -120°C or below to convert any residual austenite phase to martensite, followed by tempering to make the martensite softer, more dimensionally stable and make it amenable to machining.
  • the powder mixture contains a powder component comprising a relatively un-alloyed iron powder and a powder component comprising a steel powder containing at least some chromium or other martensite promoting element as an alloying element in addition to the pre-alloyed or diffusion bonded iron-copper powder.
  • the powder mixture may contain addition(s) of elemental martensite promoting material such as molybdenum and/or nickel for example.
  • M3/2 high speed steel powders examples are described herein, however, any other suitable tool steel or high speed steel, for example, chromium-containing steel powder may be employed depending upon the application in which the article produced therefrom is to be used.
  • An example of an alternative steel material is so-called 316 steel which is a stainless steel comprising in weight%: 17 Cr/ 2 Mo/ 13 Ni/ Bal Fe and which is substantially carbon free.
  • the composition of the iron-copper pre-alloyed or diffusion-bonded material may be any desired, e.g. iron-20 copper.
  • Powder mixtures may be made up having powder components comprising: iron; iron-copper; pre-alloyed steel powder; and, carbon powder, for example.
  • the amount of iron-copper pre-alloy powder will depend upon the final required copper content in the article and on the initial composition of the iron-copper pre-alloy powder.
  • iron-copper pre-alloyed and/or diffusion bonded material in a powder mixture together with an addition on elemental copper powder is not precluded and in some circumstances may be beneficial.
  • the use of both pre-alloyed and diffusion bonded iron-copper powder may also be employed in a powder mixture.
  • the pre-alloyed iron-copper material appears to be somewhat more effective in promoting the formation of martensite in iron grains than does diffusion bonded iron-copper material. Therefore, the use of the pre-alloyed material is preferred, however, it is pointed out that the diffusion bonded material produces martensite after sintering and subsequent processing whereas prior art infiltrated materials do not produce any martensite in the iron grain cores, the cores comprising only mixtures of pearlite and ferrite.
  • Ferrous powder mixtures of a typical composition used in the production of valve seat inserts for internal combustion engines were prepared by various routes.
  • the compositions of the powder mixtures in terms of the actual constituent component powders used to make them were as set out below in Table 1: Constituent wt % M 3/2 Graphite MoS 2 Elemental Cu Fe-Cu powder Lub Wax Fe Powder Example 1 45 0.55 1 6 47.47 0.75 - Example 1a 42.9 0.42 0.87 13 - 0.75 42.9 Example 1b 49.75 0.5 - Infiltrated - 0.75 49.75
  • Example 1 was a material prepared by the method of the present invention where all of the iron and a proportion of the copper were added as pre-alloyed iron-20 copper powder.
  • the pre-alloy powder contributes about 9.5 weight% of copper to the final material.
  • a further 6 weight% of elemental copper powder was added to the initial powder mixture to bring the total copper up to 15 weight%.
  • the steel pre-alloy powder was a water atomised M3/2 powder having a nominal composition of: 1 C; 4 Cr; 5 Mo; 3 V; 5 W. Since only 6 weight% of elemental copper powder was added, segregation was minimised.
  • Example 1a is powder mixture wherein all of the iron powder content is provided as pure iron powder and the copper content as 13 weight% of elemental copper powder. Whilst such material would not normally be made with such a high content of elemental copper powder for the reasons discussed hereinbefore, the material was made to determine the effect of the copper content on the diffusion characteristics of the chromium into the iron constituent.
  • Example 1b was made by the prior art process according to GB-A-2 188 062 wherein the copper is supplied via a simultaneous sintering and infiltration step.
  • Table 2 gives the actual compositions in terms of the constituent elements, the density of the sintered material and its final hardness following cryogenic and tempering post-sintering treatment.
  • Example 1 1.8 15.5 2.9 0.4 1.4 2.3 Bal 7.2 64-67
  • Example 1a 0.9 1.7 13 2.7 0.3 1.3
  • Example 1b 0.9 2.0 15 2.5 1.5 2.5 Bal 7.95 67-71
  • the microstructure of samples made according to Example 1 showed a tempered martensite structure even in the cores of the iron grains.
  • the martensite was formed on cooling from the sintering temperature. Cryogenic treatment was used to transform any retained austenite in the M3/2 phase of the material to martensite. The change from austenite to martensite is not easily seen under the microscope, the change being evidenced by increased hardness on the change from austenite to martensite.
  • Samples from Example 1a showed a microstructure comprising some martensite formed on cooling from the sintering temperature and retained austenite.
  • the retained austenite transformed to martensite in the M3/2 regions and the iron grains comprised mainly pearlite (a phase comprising a lamellar structure of ferrite and cementite) and some ferrite.
  • the pearlite was formed by virtue of the carbon powder added as graphite, however, owing to the absence of chromium in the iron grain cores, no martensite was formed.
  • extensive decomposition of pearlite took place and the volume fraction of ferrite increased compared with that of the as-sintered state.
  • the wear resistance of Example 1a material is inferior and the mechanical properties, as evidenced by the hardness figures, are also inferior.
  • Example 1b Samples from Example 1b demonstrated almost identical structure and properties as did Example 1a.
  • This material was made according to the known process of GB-A-2 188 062.
  • the hardness of Example 1b was slightly higher'than Example 1, this being attributed to the higher density of the material following infiltration.
  • the material of Example 1b showed extensive quantities of inherently weaker ferrite areas after tempering and not the desirable tempered martensite structure shown by Example 1 made according to the process of the present invention.
  • Figure 1 shows a histogram of valve seat insert wear of valve seat inserts, made from the material of Example 1, in the exhaust positions of a 1.81, 4-cylinder, 16-valve engine which was run for 180 hours at 6000 rev/min on unleaded gasoline, the engine having Stellite (trade name) faced valves.
  • the success criteria for this test is that valve seat insert wear must not exceed 100 ⁇ m. As may be seen from Fig.1 the maximum wear was at valve seat position 4 at 60 ⁇ m, all other inserts having wear of about 30 ⁇ m or less.
  • a powder mixture comprising 45 wt% M3/2 tool steel powder/ 0.55C/ 1 MoS 2 / 6 Cu/ 47.45 FeCu20 (diffusion bonded powder)/ 0.75 lubricating wax was made. This mixture was compacted into green compacts at 770MPa to a green density 7.1 Mgm -3 and sintered at about 1100°C under a continuous flowing nitrogen-hydrogen gas atmosphere in a conveyor furnace. The sintered articles were cryogenically treated at -120°C or below to convert retained austenite to martensite and finally tempered at 600°C. Density of the sintered material was 7.0 Mgm -3 . The hardness of the as sintered material was 61HRA; that of the cryogenically treated material 65HRA; and that of the cryogenically treated and tempered material 62-65 HRA.
  • Example 2 made with diffusion-bonded iron-copper powder) after tempering, (following sintering and cryogenic treatment) showed some small occasional areas of ferrite in the iron-rich non-tool steel phase.
  • this iron-rich phase comprised essentially pearlite rather than the extensive regions of ferrite typified by the prior art material made using the infiltration technique.
  • a mixture comprising in weight%: 75% pre-alloyed Fe-Cu20 powder/ 23% 316 stainless steel powder/ 0.75% MoS 2 powder/ 1% carbon powder was prepared; this material being coded N1.
  • the composition of the 316 stainless steel was 17 Cr/ 2 Mo/ 13 Ni/ bal Fe.
  • a comparative example coded N was made from the following mixture in weight%: 70.9% unalloyed iron powder/ 27% 316 stainless steel powder/ 0.9% MoS 2 powder/ 1.2% carbon powder. Both materials were compacted at 770MPa. However, material N1 was sintered only (as there was about 15 wt% Cu provided by the Fe-Cu pre-alloy) and material N was simultaneously sintered and infiltrated according to the known prior art process.
  • the final theoretical overall composition of both materials N1 and N in weight% was: 1 C/3.9 Cr/15 Cu/0.9 Mo/3 Ni/S 0.3/bal Fe.
  • the sintering/infiltration steps were carried out at about 1100°C under a flowing nitrogen/hydrogen atmosphere. Both materials following sintering were cryogenically treated and tempered.
  • the N1 material showed a microstructure having no ferrite, even in the cores of the grains which were predominantly iron.
  • the structure of this material showed essentially a tempered martensite structure.
  • the N material on the other hand showed extensive ferrite in the iron grains with a pearlitic structure in the transition zones between prior iron particles and 316 stainless steel particles even though this material had slightly higher carbon at 1.2%.
  • FMCA and FMCD Further mixtures denoted as material FMCA and FMCD were made according to the present invention.
  • the blend compositions of these materials in terms of the constituents in the powder mixtures are given below in Table 3.
  • FMCA FMCD Fe-20 Cu (pre-alloyed) 75 75 C 1.35 1.35 Mo 0.5 MoS 2 1 Unalloyed Fe 23.15 22.65 Lubricating wax 0.75 0.75
  • the FMCA material made according to the present invention pre-alloyed Fe-Cu powder and 0.5% elemental Mo powder were used in the initial powder mixture.
  • the FMCA material showed extensive Mo-rich zones and martensitic and bainitic areas associated with these zones.
  • the FMCA material also showed grain boundary carbides.
  • the microstructure of the FMCA material was somewhat similar to a comparative material, coded FMC (unalloyed iron powder, 1.35% C, 0.5% Mo), wherein the copper content was provided by a simultaneous sintering and infiltration process according to the prior art. Apart from the infiltration step, the sintering conditions were the same as those for the FMCA and FMCD materials.
  • the FMC material grain boundary carbide was present, the matrix was pearlite and the Mo-rich zones associated with the Mo particles were present but very small compared with the FMCA material.
  • the MoS 2 in the FMCD material undergoes partial decomposition and donates free Mo to the structure which potentially is able to generate a localised martensitic/bainitic structure associated with the Mo-rich zones. Some of the sulphur from decomposed MoS 2 reacts with iron and copper to form metallic sulphides which are beneficial for improving machinability. In the FMCD material no carbide networks could be seen and the matrix was pearlitic.
  • Figure 2 shows a graph of tool wear vs number of parts machined for FMC, FMCA and FMCD materials.
  • the Figure confirms that the materials using pre-alloyed Fe-Cu powders which give rise to extensive martensitic/bainitic areas do not have their machinability impaired in spite of the stronger, more wear resistant material structures so formed. Indeed, the machinability of the both the FMCA and FMCD materials is superior to the FMC material made by a prior art process.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Organic Chemistry (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Manufacturing & Machinery (AREA)
  • Powder Metallurgy (AREA)
  • Ceramic Products (AREA)
  • Compositions Of Oxide Ceramics (AREA)
  • Inorganic Compounds Of Heavy Metals (AREA)
  • Organic Low-Molecular-Weight Compounds And Preparation Thereof (AREA)
  • Manufacture And Refinement Of Metals (AREA)
EP02715503A 2001-01-24 2002-01-17 Process of production of a sintered ferrous material containing copper Expired - Lifetime EP1370704B1 (en)

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
GB0101770A GB0101770D0 (en) 2001-01-24 2001-01-24 Sintered ferrous material
GB0101770 2001-01-24
GB0120401A GB0120401D0 (en) 2001-08-22 2001-08-22 Sintered Ferrous Material
GB0120401 2001-08-22
PCT/GB2002/000176 WO2002059388A1 (en) 2001-01-24 2002-01-17 Sintered ferrous material containing copper

Publications (2)

Publication Number Publication Date
EP1370704A1 EP1370704A1 (en) 2003-12-17
EP1370704B1 true EP1370704B1 (en) 2005-04-27

Family

ID=26245610

Family Applications (1)

Application Number Title Priority Date Filing Date
EP02715503A Expired - Lifetime EP1370704B1 (en) 2001-01-24 2002-01-17 Process of production of a sintered ferrous material containing copper

Country Status (13)

Country Link
US (1) US20040112173A1 (ja)
EP (1) EP1370704B1 (ja)
JP (1) JP2004520486A (ja)
KR (1) KR20030070116A (ja)
CN (1) CN1314824C (ja)
AT (1) ATE294255T1 (ja)
BR (1) BR0206677A (ja)
DE (1) DE60203893T2 (ja)
ES (1) ES2237669T3 (ja)
GB (1) GB2386908B (ja)
PL (1) PL200915B1 (ja)
RU (1) RU2280706C2 (ja)
WO (1) WO2002059388A1 (ja)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20200007080A (ko) * 2017-10-30 2020-01-21 티피알 가부시키가이샤 철기 소결 합금제 밸브 가이드 및 그의 제조 방법

Families Citing this family (27)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
SE0203135D0 (sv) * 2002-10-23 2002-10-23 Hoeganaes Ab Dimensional control
GB2429464B (en) * 2005-08-23 2009-04-15 Federal Mogul Sintered Prod Manufacture of a ferrous article
ATE525156T1 (de) * 2006-07-21 2011-10-15 Hoeganaes Ab Pulver auf eisenbasis
JP5384079B2 (ja) * 2008-10-29 2014-01-08 Ｎｔｎ株式会社 焼結軸受
US9156137B2 (en) * 2010-03-01 2015-10-13 Federal State Budgetary Institution <Federal Agency for Legal Protection of Military, Special and Dual Use Intellectual Activity Results> Copper based binder for the fabrication of diamond tools
JP6141181B2 (ja) * 2010-05-19 2017-06-07 ヘガナーズ・コーポレーション 鉄粉末冶金用途における改良された寸法制御のための組成物及び方法
AT509868B1 (de) * 2010-06-10 2011-12-15 Miba Sinter Austria Gmbh Bauelement mit reduzierter metallhaftung
JP2012126972A (ja) * 2010-12-16 2012-07-05 Jfe Steel Corp 粉末冶金用合金鋼粉ならびに鉄基焼結材料およびその製造方法
KR20140123066A (ko) * 2012-01-18 2014-10-21 히타치 긴조쿠 가부시키가이샤 압분자심, 코일 부품 및 압분자심의 제조 방법
DE102012013226A1 (de) 2012-07-04 2014-01-09 Bleistahl-Produktions Gmbh & Co Kg Hochwärmeleitender Ventilsitzring
JP5859395B2 (ja) * 2012-07-27 2016-02-10 日立オートモティブシステムズ株式会社 内燃機関のピストン及びこのピストンの製造方法
CN103131930A (zh) * 2013-03-07 2013-06-05 江苏大学 一种制备粉末高速钢件的方法
JP6213809B2 (ja) * 2013-03-12 2017-10-18 日立金属株式会社 圧粉磁心、これを用いたコイル部品および圧粉磁心の製造方法
JP6194613B2 (ja) * 2013-03-29 2017-09-13 日立化成株式会社 摺動部材用鉄基焼結合金およびその製造方法
WO2015008813A1 (ja) * 2013-07-17 2015-01-22 日立金属株式会社 圧粉磁心、これを用いたコイル部品および圧粉磁心の製造方法
CN103758746B (zh) * 2014-01-17 2015-10-28 钢铁研究总院 一种钢-钢双金属转子及其制造方法
WO2017043094A1 (ja) * 2015-09-11 2017-03-16 Ｊｆｅスチール株式会社 粉末冶金用混合粉末の製造方法、焼結体の製造方法、および焼結体
CN108025357B (zh) 2015-09-18 2020-03-03 杰富意钢铁株式会社 粉末冶金用混合粉、烧结体及烧结体的制造方法
ITUA20165254A1 (it) * 2016-06-28 2017-12-28 Antonino Rinella Materiali metallici criotemprati, dotati di un'elevata capacita' di assorbire energia di deformazione elastica, destinati alla costruzione di armature di protezione per pneumatici resistenti alle perforazioni e alle lacerazioni.
CN106222566B (zh) * 2016-08-23 2018-10-09 秦皇岛市雅豪新材料科技有限公司 一种超硬材料制品专用稀土调节水雾化Fe-Cu预合金粉末及其制备方法
CN106694885B (zh) * 2016-12-15 2018-12-28 江门市佳久新材料科技有限公司 一种涡旋压缩机用粉末冶金不锈钢合金平衡块
CN106636856A (zh) * 2016-12-15 2017-05-10 江门市佳久新材料科技有限公司 一种高密度粉末冶金用不锈钢合金材料
CN107052350B (zh) * 2017-06-16 2019-10-11 大连理工大学 一种连接钨材与铜材的方法
US11794240B2 (en) 2017-11-30 2023-10-24 Gkn Sinter Metals, Llc Powder metal alloy composition for sintered powder metal insert for aluminum casting
US10780491B2 (en) 2018-01-11 2020-09-22 Ford Global Technologies, Llc Aluminum casting design with alloy set cores for improved intermetallic bond strength
DE102020213651A1 (de) * 2020-10-29 2022-05-05 Mahle International Gmbh Verschleißfeste, hochwärmeleitfähige Sinterlegierung, insbesondere für Lageranwendungen und Ventilsitzringe
CN112756608A (zh) * 2020-12-14 2021-05-07 北京有研粉末新材料研究院有限公司 一种原位生成铜包铁热管吸液芯材料的制备方法

Family Cites Families (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CH275201A (de) * 1948-07-08 1951-05-15 Plansee Metallwerk Legierter Sinterstahl.
US3583864A (en) * 1969-05-05 1971-06-08 Pfizer & Co C Chemical process of producing an iron-copper alloy powder
GB1339132A (en) * 1970-05-28 1973-11-28 Brico Eng Ferrous alloys
US3752712A (en) * 1971-06-07 1973-08-14 Domtar Ltd Iron copper prealloys
BE793539A (fr) * 1971-12-30 1973-06-29 Int Nickel Ltd Perfectionnements relatifs a la compression des poudres
US3860457A (en) * 1972-07-12 1975-01-14 Kymin Oy Kymmene Ab A ductile iron and method of making it
US4064914A (en) * 1974-05-08 1977-12-27 Union Carbide Corporation Porous metallic layer and formation
US4678510A (en) * 1985-12-24 1987-07-07 General Motors Corporation Wear resistant iron powder article
CA1337468C (en) * 1987-08-01 1995-10-31 Kuniaki Ogura Alloyed steel powder for powder metallurgy
GB8723818D0 (en) * 1987-10-10 1987-11-11 Brico Eng Sintered materials
GB8921260D0 (en) * 1989-09-20 1989-11-08 Brico Engineering Company Sintered materials
US5529604A (en) * 1995-03-28 1996-06-25 Ametek, Specialty Metal Products Division Modified stainless steel powder composition

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20200007080A (ko) * 2017-10-30 2020-01-21 티피알 가부시키가이샤 철기 소결 합금제 밸브 가이드 및 그의 제조 방법

Also Published As

Publication number Publication date
CN1488006A (zh) 2004-04-07
GB2386908A (en) 2003-10-01
ES2237669T3 (es) 2005-08-01
RU2280706C2 (ru) 2006-07-27
PL362787A1 (pl) 2004-11-02
CN1314824C (zh) 2007-05-09
EP1370704A1 (en) 2003-12-17
BR0206677A (pt) 2004-01-13
WO2002059388A1 (en) 2002-08-01
KR20030070116A (ko) 2003-08-27
US20040112173A1 (en) 2004-06-17
RU2003125845A (ru) 2005-01-27
GB0315414D0 (en) 2003-08-06
PL200915B1 (pl) 2009-02-27
DE60203893T2 (de) 2006-01-19
GB2386908B (en) 2004-09-29
DE60203893D1 (de) 2005-06-02
ATE294255T1 (de) 2005-05-15
JP2004520486A (ja) 2004-07-08

Similar Documents

Publication Publication Date Title
EP1370704B1 (en) Process of production of a sintered ferrous material containing copper
CA1337748C (en) Sintered materials
CA2725652C (en) Iron-based pre-alloyed powder
KR101245069B1 (ko) 분말 금속 기관 조성물
EP0752015B1 (en) A method of making a sintered article
US5188659A (en) Sintered materials and method thereof
EP1198601B1 (en) Sintered steel material
WO1998050593A1 (en) Method of forming a component by sintering an iron-based powder mixture
WO2002072904A1 (en) Sintered ferrous materials
EP1066128B1 (en) Metal powders obtained from residue of material removal processes on iron parts produced by chill casting
CA2549175C (en) Methods of preparing high density powder metallurgy parts by iron based infiltration

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 20030718

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT BE CH CY DE DK ES FI FR GB GR IE IT LI LU MC NL PT SE TR

AX Request for extension of the european patent

Extension state: AL LT LV MK RO SI

17Q First examination report despatched

Effective date: 20040120

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

RTI1 Title (correction)

Free format text: PROCESS OF PRODUCTION OF A SINTERED FERROUS MATERIAL CONTAINING COPPER

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AT BE CH CY DE DK ES FI FR GB GR IE IT LI LU MC NL PT SE TR

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20050427

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20050427

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20050427

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REF Corresponds to:

Ref document number: 60203893

Country of ref document: DE

Date of ref document: 20050602

Kind code of ref document: P

REG Reference to a national code

Ref country code: CH

Ref legal event code: NV

Representative=s name: KIRKER & CIE SA

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20050727

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20050727

REG Reference to a national code

Ref country code: ES

Ref legal event code: FG2A

Ref document number: 2237669

Country of ref document: ES

Kind code of ref document: T3

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20051010

NLV1 Nl: lapsed or annulled due to failure to fulfill the requirements of art. 29p and 29m of the patents act
PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20060117

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20060131

Ref country code: MC

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20060131

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

ET Fr: translation filed
26N No opposition filed

Effective date: 20060130

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: CH

Payment date: 20080108

Year of fee payment: 7

Ref country code: ES

Payment date: 20080121

Year of fee payment: 7

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: IT

Payment date: 20080119

Year of fee payment: 7

Ref country code: SE

Payment date: 20080107

Year of fee payment: 7

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: AT

Payment date: 20071212

Year of fee payment: 7

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20050427

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 20080107

Year of fee payment: 7

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20050427

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20090130

Year of fee payment: 8

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: GB

Payment date: 20081211

Year of fee payment: 8

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

EUG Se: european patent has lapsed
PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20090117

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20090131

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20090131

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST

Effective date: 20091030

REG Reference to a national code

Ref country code: ES

Ref legal event code: FD2A

Effective date: 20090119

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20090202

Ref country code: ES

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20090119

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20100117

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20100803

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20100117

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20090117

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20090118