US20040112173A1 - Sintered ferrous material contaning copper - Google Patents

Sintered ferrous material contaning copper Download PDF

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Publication number
US20040112173A1
US20040112173A1 US10/470,144 US47014403A US2004112173A1 US 20040112173 A1 US20040112173 A1 US 20040112173A1 US 47014403 A US47014403 A US 47014403A US 2004112173 A1 US2004112173 A1 US 2004112173A1
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Prior art keywords
powder
copper
iron
process according
sintered
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Abandoned
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US10/470,144
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English (en)
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Paritosh Maulik
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Federal Mogul Coventry Ltd
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Federal Mogul Sintered Products Ltd
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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
Assigned to FEDERAL-MOGUL SINTERED PRODUCTS LTD. reassignment FEDERAL-MOGUL SINTERED PRODUCTS LTD. ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: MAULIK, PARITOSH
Publication of US20040112173A1 publication Critical patent/US20040112173A1/en
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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
    • B22F3/10—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 sintered ferrous materials, articles made therefrom and to a method for their manufacture 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 manufacture of a ferrous-based sintered article containing copper in the range from 12 to 26 weight % including the steps of: making a powder mixture having a desired composition, at least a proportion of a total content of iron and copper being provided by an iron powder having copper indivisibly associated therewith; compacting said powder mixture to form a green compact of an article to be produced and sintering said green compact.
  • 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.
  • 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 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.
  • FIG. 1 shows a histogram showing wear of valve seat inserts in an engine test on material made according to the present invention
  • FIG. 2 which shows a graph of tool wear vs number of parts machined for materials made according to the present invention and prior art material.
  • 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: TABLE 1 Constit- uent Graph- Elemental Fe-Cu Lub Fe wt % M 3/2 ite MoS 2 Cu powder Wax Powder Exam- 45 0.55 1 6 47.47 0.75 — ple 1 Exam- 42.9 0.42 0.87 13 — 0.75 42.9 ple 1a Exam- 49.75 0.5 — Infil- — 0.75 49.75 ple 1b trated
  • 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.
  • 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.
  • Example 1a Samples from Example 1a showed a microstructure comprising some martensite formed on cooling from the sintering temperature and retained austenite. Following cryogenic treatment, 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.
  • FIG. 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 FeCu 20 (diffusion bonded powder)/ 0.75 lubricating wax was made. This mixture was compacted into green compacts at 770 MPa 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-Cu 20 powder/ 23% 316 stainless steel powder/ 0.75% MoS 2 powder/ 1% carbon powder was prepared; this material being coded N 1 .
  • 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 770 MPa.
  • material N 1 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 N 1 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 N 1 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%.
  • 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 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.
  • FIG. 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.

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US10/470,144 2001-01-24 2002-01-17 Sintered ferrous material contaning copper Abandoned US20040112173A1 (en)

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
GB0101770A GB0101770D0 (en) 2001-01-24 2001-01-24 Sintered ferrous material
GB0101770.6 2001-01-24
GB0120401.5 2001-08-22
GB0120401A GB0120401D0 (en) 2001-08-22 2001-08-22 Sintered Ferrous Material
PCT/GB2002/000176 WO2002059388A1 (en) 2001-01-24 2002-01-17 Sintered ferrous material containing copper

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

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DE60203893T2 (de) 2006-01-19
CN1488006A (zh) 2004-04-07
EP1370704A1 (de) 2003-12-17
CN1314824C (zh) 2007-05-09
PL200915B1 (pl) 2009-02-27
RU2003125845A (ru) 2005-01-27
PL362787A1 (pl) 2004-11-02
ES2237669T3 (es) 2005-08-01
JP2004520486A (ja) 2004-07-08
WO2002059388A1 (en) 2002-08-01
ATE294255T1 (de) 2005-05-15
GB2386908B (en) 2004-09-29
EP1370704B1 (de) 2005-04-27
BR0206677A (pt) 2004-01-13
RU2280706C2 (ru) 2006-07-27
GB0315414D0 (en) 2003-08-06

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