EP1246950B1 - Compacting and sintering steel powder - Google Patents
Compacting and sintering steel powder Download PDFInfo
- Publication number
- EP1246950B1 EP1246950B1 EP00981941A EP00981941A EP1246950B1 EP 1246950 B1 EP1246950 B1 EP 1246950B1 EP 00981941 A EP00981941 A EP 00981941A EP 00981941 A EP00981941 A EP 00981941A EP 1246950 B1 EP1246950 B1 EP 1246950B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- mpa
- compacting
- temperature
- sintering
- presintering
- 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
Links
- 238000005245 sintering Methods 0.000 title claims abstract description 22
- 239000000843 powder Substances 0.000 title claims abstract description 19
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 13
- 239000010959 steel Substances 0.000 title claims abstract description 13
- 238000000034 method Methods 0.000 claims abstract description 27
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 13
- 239000000956 alloy Substances 0.000 claims abstract description 13
- 239000000203 mixture Substances 0.000 claims abstract description 12
- 238000007792 addition Methods 0.000 claims abstract description 10
- 239000012467 final product Substances 0.000 claims abstract description 7
- 229910021529 ammonia Inorganic materials 0.000 claims abstract description 6
- 238000003825 pressing Methods 0.000 claims abstract description 4
- 238000004519 manufacturing process Methods 0.000 abstract description 3
- 239000000047 product Substances 0.000 description 14
- 238000005056 compaction Methods 0.000 description 9
- 239000002245 particle Substances 0.000 description 8
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 7
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 7
- 239000000654 additive Substances 0.000 description 4
- 229910052802 copper Inorganic materials 0.000 description 4
- 239000010949 copper Substances 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 229910052759 nickel Inorganic materials 0.000 description 4
- 230000000754 repressing effect Effects 0.000 description 4
- 229910001369 Brass Inorganic materials 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 3
- 238000000137 annealing Methods 0.000 description 3
- 239000010951 brass Substances 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 230000006835 compression Effects 0.000 description 2
- 238000007906 compression Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 238000000280 densification Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 230000001681 protective effect Effects 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- JZQOJFLIJNRDHK-CMDGGOBGSA-N alpha-irone Chemical compound CC1CC=C(C)C(\C=C\C(C)=O)C1(C)C JZQOJFLIJNRDHK-CMDGGOBGSA-N 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000008030 elimination Effects 0.000 description 1
- 238000003379 elimination reaction Methods 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 239000011265 semifinished product Substances 0.000 description 1
- 239000011343 solid material Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- BPJYAXCTOHRFDQ-UHFFFAOYSA-L tetracopper;2,4,6-trioxido-1,3,5,2,4,6-trioxatriarsinane;diacetate Chemical compound [Cu+2].[Cu+2].[Cu+2].[Cu+2].CC([O-])=O.CC([O-])=O.[O-][As]1O[As]([O-])O[As]([O-])O1.[O-][As]1O[As]([O-])O[As]([O-])O1 BPJYAXCTOHRFDQ-UHFFFAOYSA-L 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Classifications
-
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/12—Both compacting and sintering
- B22F3/16—Both compacting and sintering in successive or repeated steps
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
Definitions
- the invention concerns a method of getting shaped elements by compaction, sintering and repressing of a steel powder mixtures with alloy additives, being used for production of machine parts, e.g. gears, bearings and others of high wear resistance and surface strength.
- Densification of powders during compaction in a closed die under pressure is performed as a result of mutual interparticle shear and plastic deformation of the powder particles. Their bonding at the definite stage of compaction arrests the interparticle shear process. So, further increasing of product density can take place only due to the deformation of powder particles. Intensive cold hardening of being pressed particles occurs. Further increasing compaction force is needed to deform a such powdered body and to overcome outside friction forces at the contact of powder material and a compaction tool. The result is to get high porosity after single compaction in the range from 15% to 20%.
- Plastic deformation of a presintered semi-final product follows forming and shift of dislocations through crystal lattice at the definite slip planes.
- Plasticity and particularly densification ability of such sintered product increase if, during first sintering, the elimination of structure elements (solid solutions, fine-grained particles, secondary phases, etc.) inhibiting dislocations' movement is achieved. That is why the first sintering should be conducted in conditions of recrystallization annealing at temperature A cl .
- the steel powder green compacts consist of a mixture of different components such as iron powder (or an alloyed iron powder) and graphite additives.
- the optimal presintering temperature of green compacts should in the range of 720 °C to 730 °C., A solubility of carbon in ⁇ -iron at this temperature range is about 0.03%, and the product after presintering is characterised by low yield strength and hardening coefficients as a result of lack of such strengthening factors as secondary phases, particle dispersability, etc.
- the bonding contact points may be generally defined by positions of atoms belonging to both powder particles, separated with interparticle boundaries. An assembly of such contact points may be identified with "space contact lattice".
- the formation of interparticle interaction areas takes place not only as a result of "space contact lattice” motion along interparticle surfaces but also by verging of "space contact lattice” parameters towards matrix crystal lattice parameters. If a dissolving of carbon and alloy additions in iron at 720 °C - 730 °C does not take place, then parameters of "space contact lattice" can be changed in wide range by varying time of sintering at above temperatures.
- interparticle contact points make a system of glide planes, which is used as a system of glide planes inside grains and particles at ambient (room) temperature. Gliding along interparticle connections takes place under outside presssure, what has an essential importance to the process of plastic strain.
- Similar model can be called a model for "super dislocation” because it is based on an effective gliding along particle boundaries as a result of particular shift kind of "space contact lattice”. This leads to additional, significant increase of sintered semi-final product palsticity, because it is known that metal material plasticity increases significantly if an additional mechanism of plastic strain, besides gliding at dislocation shift, is introduced into a process of plastic metal flow.
- the essence of the invention concerning a method of getting shaped elements by pressing, sintering and compacting of powder mixtures of steel with alloy additions, consists in that a preformed element is treated with presintering, preferably in dissociated-ammonia atmosphere at temperature 700 - 750 °C, preferably 720 - 730 °C, during 20 - 40 min, preferably 30 min, and first compacting under pressure 700 - 800 MPa, preferably 750 MPa, and then second compacting with simultaneous calibration under pressure 900 - 1000 MPa, preferably 950 MPa, then final sintering at temperature 1100 - 1200 °C, preferably 1120 - 1150 °C, during 40 - 50 min, preferably 45 min.
- Preformed semi-final product from powder mixtures of steel with alloy additions of brass, nickel, copper, and others is treated with presintering in dissociated-ammonia atmosphere at temperature 725 ⁇ 5 °C during 30 min, and treated with compacting under pressure 750 MPa. Then it is treated with second compacting under pressure 950 MPa and calibration, then final sintering at temperature 1130 °C during 45 min.
- Preformed semi-final product from powder mixtures of steel with alloy additions of brass, nickel, copper, and others is treated with presintering in dissociated-ammonia atmosphere at temperature 740 ⁇ 5 °C during 25 min, and first compacting under pressure 780 MPa. So prepared element is treated with second compacting under pressure 980 MPa and calibration, then final sintering at temperature 1180 °C during 40 min.
- Preformed semi-final product from powder mixtures of steel with alloy additions of brass, nickel, copper, and others is treated with presintering in dissociated-ammonia atmosphere at temperature 710 ⁇ 5 °C during 35 min, and first compacting under pressure 710 MPa, then it is treated with second compacting under pressure 910 MPa and calibration, then final sintering at temperature 1100 °C during 50 min.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Powder Metallurgy (AREA)
- Mechanical Treatment Of Semiconductor (AREA)
- Processing Of Stones Or Stones Resemblance Materials (AREA)
Abstract
Description
- The invention concerns a method of getting shaped elements by compaction, sintering and repressing of a steel powder mixtures with alloy additives, being used for production of machine parts, e.g. gears, bearings and others of high wear resistance and surface strength.
- In well-known solutions, structural parts from powder mixtures with alloy additives are made by compaction and sintering at temperature 1100 - 1150 °C in a protective atmosphere. Products obtained by this method are characterized by high porosity up to 12% of volume and low compression strength.
- In other method, a product from powder alloy steel is double pressed and double sintered at temperatures 800 °C and 1150 °C. In this solution, obtained products also do not get required high strength parameters.
- There is also known a method of getting structural parts from steel powder mixtures with alloy additions, consisting in compaction, presintering at the temperature 800 - 850 °C, repressing of presintered semi-finished product and final sintering at the temperature 1120 - 1180 °C in a protective atmosphere. Parts obtained by this method have insufficient strength parameters, in particular low bending strength. A similar method is disclosed in EP-0 457 418 A1.
- Moreover there is known a method of getting parts from metal powders with alloy additions, where compaction , presintering at temperature 650 °C, second pressing (repressing) and second sintering at temperature 1150 °C are carried out. Parts obtained by this method are characterized by low strength parameters, in particular low radial compression strength of ring products.
- Presented above methods of getting products of steel powder mixtures with alloy additives do not precise pressure values that are to act onto shaped part, as well as they do not specify exact time during which sintering should be performed, giving a very wide temperature range.
- Densification of powders during compaction in a closed die under pressure is performed as a result of mutual interparticle shear and plastic deformation of the powder particles. Their bonding at the definite stage of compaction arrests the interparticle shear process. So, further increasing of product density can take place only due to the deformation of powder particles. Intensive cold hardening of being pressed particles occurs. Further increasing compaction force is needed to deform a such powdered body and to overcome outside friction forces at the contact of powder material and a compaction tool. The result is to get high porosity after single compaction in the range from 15% to 20%.
- Further increasing of product density can be obtained due to decreasing of metal flow stress and increasing of a compact plasticity, which may be achieved during presintering at temperatures equal to annealing temperature of a definite metal. So the process of presintering at annealing temperature makes possible to increase product density through its plastic deformation during repressing operation.
- Plastic deformation of a presintered semi-final product, like for solid material, follows forming and shift of dislocations through crystal lattice at the definite slip planes. Plasticity and particularly densification ability of such sintered product, increase if, during first sintering, the elimination of structure elements (solid solutions, fine-grained particles, secondary phases, etc.) inhibiting dislocations' movement is achieved. That is why the first sintering should be conducted in conditions of recrystallization annealing at temperature Acl.
- The steel powder green compacts consist of a mixture of different components such as iron powder (or an alloyed iron powder) and graphite additives. The optimal presintering temperature of green compacts should in the range of 720 °C to 730 °C., A solubility of carbon in α-iron at this temperature range is about 0.03%, and the product after presintering is characterised by low yield strength and hardening coefficients as a result of lack of such strengthening factors as secondary phases, particle dispersability, etc.
- It is well-known that diffusive mobility of iron atoms in carbon steels in state before transformation (for structural steels with alloyed elements of Cr, Mo, Ni, Cu) at 720 °C - 730 °C is approximately of the same value as in γ-iron at 1100 °C - 1200 °C.
- During presintering diffusion processes of iron atoms in the range of temperatures 720 °C - 730 °C result in formation of interparticle bonding focuses (contact points).
- The bonding contact points may be generally defined by positions of atoms belonging to both powder particles, separated with interparticle boundaries. An assembly of such contact points may be identified with "space contact lattice". The formation of interparticle interaction areas takes place not only as a result of "space contact lattice" motion along interparticle surfaces but also by verging of "space contact lattice" parameters towards matrix crystal lattice parameters. If a dissolving of carbon and alloy additions in iron at 720 °C - 730 °C does not take place, then parameters of "space contact lattice" can be changed in wide range by varying time of sintering at above temperatures.
- After definite time of sintering, interparticle contact points make a system of glide planes, which is used as a system of glide planes inside grains and particles at ambient (room) temperature. Gliding along interparticle connections takes place under outside presssure, what has an essential importance to the process of plastic strain. Similar model can be called a model for "super dislocation" because it is based on an effective gliding along particle boundaries as a result of particular shift kind of "space contact lattice". This leads to additional, significant increase of sintered semi-final product palsticity, because it is known that metal material plasticity increases significantly if an additional mechanism of plastic strain, besides gliding at dislocation shift, is introduced into a process of plastic metal flow.
- Taking into account above-mentioned conditions, a method being a subject of the invention has been developed.
- The essence of the invention, concerning a method of getting shaped elements by pressing, sintering and compacting of powder mixtures of steel with alloy additions, consists in that a preformed element is treated with presintering, preferably in dissociated-ammonia atmosphere at temperature 700 - 750 °C, preferably 720 - 730 °C, during 20 - 40 min, preferably 30 min, and first compacting under pressure 700 - 800 MPa, preferably 750 MPa, and then second compacting with simultaneous calibration under pressure 900 - 1000 MPa, preferably 950 MPa, then final sintering at temperature 1100 - 1200 °C, preferably 1120 - 1150 °C, during 40 - 50 min, preferably 45 min.
- Thanks to use of the method according to the invention, the following technical-and-operational effects were gained:
- high wear, crushing, shear and compressive strength of got product
- high yield point,
- density of got product above 7.6 g/cm3,
- low material flow coefficient, in the range 10-2 - 10-3 mm,
- decrease of production power consumption,
- possible use for products of optional shapes, optional application, especially for products of required high strength as gears, bearings, etc.
- Subject of the invention is shown in the following exemplary embodiments:
- Preformed semi-final product from powder mixtures of steel with alloy additions of brass, nickel, copper, and others is treated with presintering in dissociated-ammonia atmosphere at temperature 725±5 °C during 30 min, and treated with compacting under pressure 750 MPa. Then it is treated with second compacting under pressure 950 MPa and calibration, then final sintering at temperature 1130 °C during 45 min.
- Preformed semi-final product from powder mixtures of steel with alloy additions of brass, nickel, copper, and others is treated with presintering in dissociated-ammonia atmosphere at temperature 740±5 °C during 25 min, and first compacting under pressure 780 MPa. So prepared element is treated with second compacting under pressure 980 MPa and calibration, then final sintering at temperature 1180 °C during 40 min.
- Preformed semi-final product from powder mixtures of steel with alloy additions of brass, nickel, copper, and others is treated with presintering in dissociated-ammonia atmosphere at temperature 710±5 °C during 35 min, and first compacting under pressure 710 MPa, then it is treated with second compacting under pressure 910 MPa and calibration, then final sintering at temperature 1100 °C during 50 min.
- In the enclosed table, the results of strength tests of parts made from powder mixtures of steel with alloy additions, made with the method according to the invention at different temperatures of the first sintering compared with standard sample made with hitherto method.
Claims (7)
- A method of getting shaped elements by sintering and pressing, of powder mixtures of steel with alloy additions, in which a preformed semi-final product is treated with presintering, and first compacting under pressure 700 - 800 MPa, and then second compacting with simultaneous calibration under pressure 900 - 1000 MPa, then treated with final sintering at temperature 1100 - 1200 °C,
- A method according to claim 1, characterized in that the presintering treatment is carried out in dissociated-ammonia atmosphere at temperature 700 - 750 °C, preferably 720 - 730 °C.
- A method according to claim 2, characterized in that the presintering treatment is carried out during 20-40 min, preferably 30 min.
- A method according to any of the claims 1 to 3, characterized in that the first compacting pressure is 750 mPa.
- A method according to any of the claims 1 to 4, characterized in that the second compacting pressure is 950 mPa.
- A method according to any of the claims 1 to 5, characterized in that the final sintering temperature is 1120-1150°C.
- A method according to any of the claims 1 to 6, characterized in that final sintering is carried out during 40 - 50 min, preferably 45 min.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| PL33763799 | 1999-12-31 | ||
| PL337637A PL191806B1 (en) | 1999-12-31 | 1999-12-31 | Method of obtaining shaped workpieces |
| PCT/PL2000/000098 WO2001049891A1 (en) | 1999-12-31 | 2000-12-14 | Compacting and sintering steel powder |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| EP1246950A1 EP1246950A1 (en) | 2002-10-09 |
| EP1246950B1 true EP1246950B1 (en) | 2003-07-23 |
Family
ID=20075799
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| EP00981941A Expired - Lifetime EP1246950B1 (en) | 1999-12-31 | 2000-12-14 | Compacting and sintering steel powder |
Country Status (5)
| Country | Link |
|---|---|
| EP (1) | EP1246950B1 (en) |
| AT (1) | ATE245715T1 (en) |
| DE (1) | DE60004106T2 (en) |
| PL (1) | PL191806B1 (en) |
| WO (1) | WO2001049891A1 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE102004002714B3 (en) * | 2004-01-19 | 2005-05-19 | SCHWäBISCHE HüTTENWERKE GMBH | To produce sintered components, of light metal alloys, the powder is compressed into a green compact to be give a low temperature sintering followed by further compression and high temperature sintering |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2648519B2 (en) * | 1989-10-03 | 1997-09-03 | 日立粉末冶金株式会社 | Method of manufacturing synchronizer hub |
| US5080712B1 (en) * | 1990-05-16 | 1996-10-29 | Hoeganaes Corp | Optimized double press-double sinter powder metallurgy method |
| WO1997043066A1 (en) * | 1996-05-13 | 1997-11-20 | The Presmet Corporation | Method for preparing high performance ferrous materials |
-
1999
- 1999-12-31 PL PL337637A patent/PL191806B1/en unknown
-
2000
- 2000-12-14 EP EP00981941A patent/EP1246950B1/en not_active Expired - Lifetime
- 2000-12-14 WO PCT/PL2000/000098 patent/WO2001049891A1/en active IP Right Grant
- 2000-12-14 AT AT00981941T patent/ATE245715T1/en not_active IP Right Cessation
- 2000-12-14 DE DE60004106T patent/DE60004106T2/en not_active Expired - Lifetime
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE102004002714B3 (en) * | 2004-01-19 | 2005-05-19 | SCHWäBISCHE HüTTENWERKE GMBH | To produce sintered components, of light metal alloys, the powder is compressed into a green compact to be give a low temperature sintering followed by further compression and high temperature sintering |
Also Published As
| Publication number | Publication date |
|---|---|
| EP1246950A1 (en) | 2002-10-09 |
| WO2001049891A1 (en) | 2001-07-12 |
| PL191806B1 (en) | 2006-07-31 |
| ATE245715T1 (en) | 2003-08-15 |
| PL337637A1 (en) | 2001-07-02 |
| DE60004106T2 (en) | 2004-04-22 |
| DE60004106D1 (en) | 2003-08-28 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US5080712A (en) | Optimized double press-double sinter powder metallurgy method | |
| EP1395383A1 (en) | High density stainless steel products and method for the preparation thereof | |
| EP0202886B1 (en) | Canless method for hot working gas atomized powders | |
| EP1246950B1 (en) | Compacting and sintering steel powder | |
| EP0200691B1 (en) | Iron-based powder mixture for a sintered alloy | |
| US5561832A (en) | Method for manufacturing vanadium carbide powder added tool steel powder by milling process, and method for manufacturing parts therewith | |
| JP4060092B2 (en) | Alloy steel powder for powder metallurgy and sintered body thereof | |
| EP0011981B1 (en) | Method of manufacturing powder compacts | |
| JPS6345306A (en) | Production of sintered member | |
| JP2932538B2 (en) | Manufacturing method of alloy material for molding bullets | |
| US4603028A (en) | Method of manufacturing sintered components | |
| CA1136445A (en) | Method for producing hot forged material from powder | |
| Wang | Properties of high density powder forged iron based alloy | |
| Kandavel et al. | Experimental Investigations on Plastic Deformation and Densification Characteristics of P/M Fe–C–Cu–Mo Alloy Steels Under Cold Upsetting | |
| JPH032335A (en) | Manufacture of titanium powder or titanium alloy powder sintered product | |
| SU1740108A1 (en) | Method for making articles from powdered structural steels | |
| JPH04131334A (en) | Production of alloy for shaped charge | |
| US20030047032A1 (en) | Method of producing powder metal parts from metallurgical powders including sponge iron | |
| JPH0499805A (en) | Complex hard sintered material having excellent wear resistance and melt-welding resistance and manufacture thereof | |
| Zhou et al. | Rotary forging of sintered iron based composites | |
| JPS55138055A (en) | Sintered alloy having lubrication function, preparation of the same, and friction mate-material using the same | |
| JPH05271851A (en) | Production of fe-base sintered alloy member having high strength and high toughness | |
| JP2741256B2 (en) | Low thermal expansion sintered alloy, method for producing the same, and compression apparatus | |
| JPH0578712A (en) | Production of sintered part | |
| Gessinger et al. | Effect of deformation on mechanical properties of high temperature P/M steel |
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 |
|
| 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 |
|
| 17P | Request for examination filed |
Effective date: 20020718 |
|
| GRAH | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOS IGRA |
|
| GRAH | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOS IGRA |
|
| GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
| AK | Designated contracting states |
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: IT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT;WARNING: LAPSES OF ITALIAN PATENTS WITH EFFECTIVE DATE BEFORE 2007 MAY HAVE OCCURRED AT ANY TIME BEFORE 2007. THE CORRECT EFFECTIVE DATE MAY BE DIFFERENT FROM THE ONE RECORDED. Effective date: 20030723 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: 20030723 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: 20030723 Ref country code: AT 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: 20030723 Ref country code: CH 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: 20030723 Ref country code: FR 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: 20030723 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: 20030723 Ref country code: LI 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: 20030723 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: 20030723 |
|
| 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: 60004106 Country of ref document: DE Date of ref document: 20030828 Kind code of ref document: P |
|
| 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 FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20031023 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: 20031023 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: 20031023 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: ES 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: 20031103 |
|
| 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: 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: 20031214 Ref country code: LU Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20031214 |
|
| 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: 20031215 |
|
| 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: 20031223 |
|
| PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: MC Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20031231 |
|
| REG | Reference to a national code |
Ref country code: CH Ref legal event code: PL |
|
| 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 |
|
| 26N | No opposition filed |
Effective date: 20040426 |
|
| EN | Fr: translation not filed | ||
| REG | Reference to a national code |
Ref country code: IE Ref legal event code: MM4A |
|
| 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: 20041214 |
|
| GBPC | Gb: european patent ceased through non-payment of renewal fee |
Effective date: 20041214 |
|
| PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DE Payment date: 20151208 Year of fee payment: 16 |
|
| REG | Reference to a national code |
Ref country code: DE Ref legal event code: R119 Ref document number: 60004106 Country of ref document: DE |
|
| 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: 20170701 |