CA2084679C - Iron-based powder, component produced therefrom, and method of producing the component - Google Patents
Iron-based powder, component produced therefrom, and method of producing the component Download PDFInfo
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- CA2084679C CA2084679C CA002084679A CA2084679A CA2084679C CA 2084679 C CA2084679 C CA 2084679C CA 002084679 A CA002084679 A CA 002084679A CA 2084679 A CA2084679 A CA 2084679A CA 2084679 C CA2084679 C CA 2084679C
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- iron
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- 239000000843 powder Substances 0.000 title claims abstract description 38
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 title claims abstract description 34
- 229910052742 iron Inorganic materials 0.000 title claims abstract description 14
- 238000000034 method Methods 0.000 title claims abstract description 14
- 238000005245 sintering Methods 0.000 claims abstract description 25
- 238000005275 alloying Methods 0.000 claims abstract description 19
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 3
- 239000010959 steel Substances 0.000 claims abstract description 3
- VAKIVKMUBMZANL-UHFFFAOYSA-N iron phosphide Chemical compound P.[Fe].[Fe].[Fe] VAKIVKMUBMZANL-UHFFFAOYSA-N 0.000 claims description 4
- 239000000306 component Substances 0.000 abstract 2
- 229910052729 chemical element Inorganic materials 0.000 abstract 1
- 239000000463 material Substances 0.000 description 18
- 239000011148 porous material Substances 0.000 description 6
- 229910052750 molybdenum Inorganic materials 0.000 description 5
- 230000000694 effects Effects 0.000 description 4
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- 230000002411 adverse Effects 0.000 description 2
- 238000009792 diffusion process Methods 0.000 description 2
- 239000007791 liquid phase Substances 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 1
- 229910002056 binary alloy Inorganic materials 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- -1 phosphor com-pound Chemical class 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000003381 stabilizer Substances 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 238000009692 water atomization Methods 0.000 description 1
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
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
-
- 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
- C22C33/0264—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements the maximum content of each alloying element not exceeding 5%
-
- 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
- C22C33/0214—Using a mixture of prealloyed powders or a master alloy comprising P or a phosphorus compound
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Powder Metallurgy (AREA)
- Soft Magnetic Materials (AREA)
- Superconductors And Manufacturing Methods Therefor (AREA)
- Hard Magnetic Materials (AREA)
Abstract
An iron-based powder for producing impact-resistant compo-nents by powder compacting and sintering contains, in addition to Fe, 0.3-0.7 % by weight of P, 0.3-3.5 % by weight of Mo, and not more than 2 by weight of other alloying elements.
A method of powder-metatlurgicalty producing impact-resistant steel components comprises using an ir-on-based powder which, in addition to Fe, contains 0.3-0.7 % by weight of P, preferably 0.35-0.65 % by weight of P, 0.3-3.5 % by weight of Mo, preferably 0.5-2.5 % by weight of Mo, and not more than 2 % by weight, preferably not more than 1 by weight, of other alloying ele-ments; compacting the powder into the desired shape; and sintering the compact.
A method of powder-metatlurgicalty producing impact-resistant steel components comprises using an ir-on-based powder which, in addition to Fe, contains 0.3-0.7 % by weight of P, preferably 0.35-0.65 % by weight of P, 0.3-3.5 % by weight of Mo, preferably 0.5-2.5 % by weight of Mo, and not more than 2 % by weight, preferably not more than 1 by weight, of other alloying ele-ments; compacting the powder into the desired shape; and sintering the compact.
Description
,.. W09t/t9582 PGT/SE91/004f14 IRON-BASED POWDER] COMPONENT PRODUCED THEREFROM, AND
METHOD OF PRODVCING TH~ COMPONENT
The present invention relates to an iron-based powder far producing impact-resistant components by powder com-pacting and sintering.
The invention also concerns a powder-metallurgically produced component made from this powder. Finally, the invention bears upon a method of powder-metallurgically producing such a component.
The remaining porosity of sintered powder-metallur-gical materials impairs the mechanical properties of the materials, as compared with completely dense materials.
This is a result of the pores acting as stress concentra-tions, as well as reducing the effective volume under stress. Thus, strength, ductility, fatigue strength, macro-hardness etc. in iron-based powder-metallurgical materials decrease as the porosity increases. Impact energy is, however, the property the most adversely affected.
Despite their impaired impact energy, iron-based powder-metallurgical materials are, to a certain extent, used in components requiring high impact energy. Natural-ly, this necessitates high precision when manufacturing td~e components, the effect of the porosity on impact energy being well-known.
The impact energy of sintered steel may be increased by alloying with Ni, which augments the strength and duc-tility of the material and, furthermore, causes shrinkage of the material, i.e. a density increase. The effect of Ni-alloying is especially pronounced when the sintering is carried out at a high temperature, i.e. above 1150°C.
Naturally, the high temperature results in a more active sintering and produces rounder pores than do low sintering temperatures. In addition, the rounder pores also increase the impact energy. Alternatively, a more active sintering can be achieved by adding P, which increases strength and ~'~'~ WO 91/19582 2 0 8 4 6'7 9 P~T/SE91/004(~4 ductility, as well as rounds off the pores even at lower sintering temperatures, 1.e. below 1150°C.
To sum up, the impact energy of sintered materials ' can be increased by reducing the stress concentration effect of the pores. This can be achieved by liquid-phase ' sintering, high-temperature sintering, sintering of a ferritic material, double compacting, and by adding alloy-ing elements having a shrinking effect.
In many cases, however; sufficient impact energy is only achieved with a combination of the above measures, which usually requires extensive and costly processing when using alloying systems known in the powder-metallur-gieal techniques of today.
The object of the present invention is, therefore, to provide an iron-based powder which simplifies the process-ing, yet yields sufficiently impact-resistant components by powder compacting and sintering.
It is further desired that simple powder compacting as well as sintering can be carried out in a belt furnace, i.e. at temperatures below about 1150°C.
This object is achieved by an iron-based powder which, in addition to Fe, contains Mo and P, and in which the content of other alloying elements is maintained on a low level. This material is, inter alia, characterised by the fact that sintering even below 1150°C results in an impact energy which is higher than that of today's powder-metallurgical materials sintered at higher temperatures.
Further, the material has excellent compressibility and is capable of considerable shrinkage, giving a sintered mate- ' rial of high density. For one and the same density, the material of the invention further has a substantially higher impact energy than today's powder-metallurgical materials.
The amount of Mo in the material should be 0.3-3.5$
by weight, preferably 0.5-2.5$ by weight, and the amount of P should be 0.3-0.7$ by weight, preferably 0.35-0.65$
by weight, most preferably 0.4-0.6$ by Weight. Further, the amount of other alloying elements should not exceed 2%
by weight, preferably not 1% by weight, and most preferably not 0.5% by weight. In addition, C may be present in a maximum amount of 0.1% by weight, preferably 0.07% by weight.
The invention provides an iron-based powder for producing impact-resistant components by powder compacting and sintering, which powder contains, in addition to Fe, 0.3-0.7% by weight of P, 0.3-3.5% by weight of Mo, and not more than 2% by weight of other alloying elements, optionally including a maximum of 0.1% by weight of C.
This powder can be produced by making a base powder of pure Fe, or Fe and Mo in solid solution. This can be produced either as a water-atomised powder or as a sponge powder. Suitably, the base powder is annealed in a reducing atmosphere to lower the content of impurities. Then, the powder is mixed with P, or Mo and P, and is compacted into the desired shape, whereupon sintering is carried out a temperature which advantageously is below 1150°C.
Example A base powder of Fe containing 1.5 by weight of Mo was prepared by water-atomisation. Then, 0.5% by weight of P
was added. Test pieces were produced by compacting at a pressure of 4-8 ton/cmz. The test pieces were sintered at 1120°C for 30 min. The resulting densities and impact energies are apparent from the upper curve in 2 Fig. 1, where the compacting pressure in ton/cmz is the parameter. For instance, an impact energy of 180 J and a 2 density of 7.46 g/cm2 were obtained at a compacting pressure of 8 ton/cm2.
METHOD OF PRODVCING TH~ COMPONENT
The present invention relates to an iron-based powder far producing impact-resistant components by powder com-pacting and sintering.
The invention also concerns a powder-metallurgically produced component made from this powder. Finally, the invention bears upon a method of powder-metallurgically producing such a component.
The remaining porosity of sintered powder-metallur-gical materials impairs the mechanical properties of the materials, as compared with completely dense materials.
This is a result of the pores acting as stress concentra-tions, as well as reducing the effective volume under stress. Thus, strength, ductility, fatigue strength, macro-hardness etc. in iron-based powder-metallurgical materials decrease as the porosity increases. Impact energy is, however, the property the most adversely affected.
Despite their impaired impact energy, iron-based powder-metallurgical materials are, to a certain extent, used in components requiring high impact energy. Natural-ly, this necessitates high precision when manufacturing td~e components, the effect of the porosity on impact energy being well-known.
The impact energy of sintered steel may be increased by alloying with Ni, which augments the strength and duc-tility of the material and, furthermore, causes shrinkage of the material, i.e. a density increase. The effect of Ni-alloying is especially pronounced when the sintering is carried out at a high temperature, i.e. above 1150°C.
Naturally, the high temperature results in a more active sintering and produces rounder pores than do low sintering temperatures. In addition, the rounder pores also increase the impact energy. Alternatively, a more active sintering can be achieved by adding P, which increases strength and ~'~'~ WO 91/19582 2 0 8 4 6'7 9 P~T/SE91/004(~4 ductility, as well as rounds off the pores even at lower sintering temperatures, 1.e. below 1150°C.
To sum up, the impact energy of sintered materials ' can be increased by reducing the stress concentration effect of the pores. This can be achieved by liquid-phase ' sintering, high-temperature sintering, sintering of a ferritic material, double compacting, and by adding alloy-ing elements having a shrinking effect.
In many cases, however; sufficient impact energy is only achieved with a combination of the above measures, which usually requires extensive and costly processing when using alloying systems known in the powder-metallur-gieal techniques of today.
The object of the present invention is, therefore, to provide an iron-based powder which simplifies the process-ing, yet yields sufficiently impact-resistant components by powder compacting and sintering.
It is further desired that simple powder compacting as well as sintering can be carried out in a belt furnace, i.e. at temperatures below about 1150°C.
This object is achieved by an iron-based powder which, in addition to Fe, contains Mo and P, and in which the content of other alloying elements is maintained on a low level. This material is, inter alia, characterised by the fact that sintering even below 1150°C results in an impact energy which is higher than that of today's powder-metallurgical materials sintered at higher temperatures.
Further, the material has excellent compressibility and is capable of considerable shrinkage, giving a sintered mate- ' rial of high density. For one and the same density, the material of the invention further has a substantially higher impact energy than today's powder-metallurgical materials.
The amount of Mo in the material should be 0.3-3.5$
by weight, preferably 0.5-2.5$ by weight, and the amount of P should be 0.3-0.7$ by weight, preferably 0.35-0.65$
by weight, most preferably 0.4-0.6$ by Weight. Further, the amount of other alloying elements should not exceed 2%
by weight, preferably not 1% by weight, and most preferably not 0.5% by weight. In addition, C may be present in a maximum amount of 0.1% by weight, preferably 0.07% by weight.
The invention provides an iron-based powder for producing impact-resistant components by powder compacting and sintering, which powder contains, in addition to Fe, 0.3-0.7% by weight of P, 0.3-3.5% by weight of Mo, and not more than 2% by weight of other alloying elements, optionally including a maximum of 0.1% by weight of C.
This powder can be produced by making a base powder of pure Fe, or Fe and Mo in solid solution. This can be produced either as a water-atomised powder or as a sponge powder. Suitably, the base powder is annealed in a reducing atmosphere to lower the content of impurities. Then, the powder is mixed with P, or Mo and P, and is compacted into the desired shape, whereupon sintering is carried out a temperature which advantageously is below 1150°C.
Example A base powder of Fe containing 1.5 by weight of Mo was prepared by water-atomisation. Then, 0.5% by weight of P
was added. Test pieces were produced by compacting at a pressure of 4-8 ton/cmz. The test pieces were sintered at 1120°C for 30 min. The resulting densities and impact energies are apparent from the upper curve in 2 Fig. 1, where the compacting pressure in ton/cmz is the parameter. For instance, an impact energy of 180 J and a 2 density of 7.46 g/cm2 were obtained at a compacting pressure of 8 ton/cm2.
A test piece produced in the manner described above, but without Mo, had a much lower impact energy, as is apparent from the lower curve in Fig. 1.
At high-temperature sintering, the material shrinks more, which leads to higher density and, consequently, to higher impact energy. This is illustrated by the point A on the upper curve in Fig. l, which was obtained at a compacting pressure of 6 ton/cm2 and by sintering at 1250°C for 30 min.
It should be observed that the combined addition of P and Mo results in a higher sintered density than does a binary system of Fe and P, even if subjected to double compacting. For one and the same density, the material of the invention further gives a much higher impact energy, - 3a -which in all probability should be attributed to a more active sintering and a positive interaction between Mo arid P.
A powder according to the inventiGn containing 1.5%
by weight of Mo and varying amounts of F in the range of 0-0.8% by weight was produced. Test pieces were made by compacting at 589 MPa and sintering at 1120°C. The result-ing impact energy in J is apparent from Fig. 2. As shown therein, a maximum value is achieved at 0.5% by weight of P; good values are obtained in the range of 0.3-0.7% by weight of P; even better values are obtained in the range of 0.35-0.65% by weight of P; and the best values are obtained in the range of 0.4-0.6% by weight of P.
Similarly, a powder containing 0.5% by weight of P and varying amounts of Mo in the range of 0-4% by weight was produced. Test pieces were produced by compacting at 589 MPa and sintering at 1120°C. The resulting impact energy values are apparent from Fig. 3. As shown therein, 0.3-3.5% by weight of Mo constitutes a useful range, whereas 0.5-2.5% by weight of Mo constitutes a preferred range.
Very likely, the results obtained are due to the fol-lowing. The addition of P entails that a liquid phase is obtained during sintering at a comparatively low tempera-Lure, resulting in a better distribution of P in the mate-rial. P diffuses into the iron particles, and, to some extent, austenite is transformed to ferrite, which faci-litates the diffusion of Mo. Both P and Mo are ferrite stabilisers, and the transformation to ferrite increases the self-diffusion of Fe. This gives an active sintering, resulting in shrinkage and round pores.
Suitably, P is present in the form of a phosphor com-pound, preferably iron phosphide, e.g. Fe3P.
The other alloying elements may be of a type not affecting the impact energy adversely, and common in pow-der metallurgy. As non-restrictive examples, mention may be made of Ni, W, Mn and Cr. Cu should not be used at all.
At high-temperature sintering, the material shrinks more, which leads to higher density and, consequently, to higher impact energy. This is illustrated by the point A on the upper curve in Fig. l, which was obtained at a compacting pressure of 6 ton/cm2 and by sintering at 1250°C for 30 min.
It should be observed that the combined addition of P and Mo results in a higher sintered density than does a binary system of Fe and P, even if subjected to double compacting. For one and the same density, the material of the invention further gives a much higher impact energy, - 3a -which in all probability should be attributed to a more active sintering and a positive interaction between Mo arid P.
A powder according to the inventiGn containing 1.5%
by weight of Mo and varying amounts of F in the range of 0-0.8% by weight was produced. Test pieces were made by compacting at 589 MPa and sintering at 1120°C. The result-ing impact energy in J is apparent from Fig. 2. As shown therein, a maximum value is achieved at 0.5% by weight of P; good values are obtained in the range of 0.3-0.7% by weight of P; even better values are obtained in the range of 0.35-0.65% by weight of P; and the best values are obtained in the range of 0.4-0.6% by weight of P.
Similarly, a powder containing 0.5% by weight of P and varying amounts of Mo in the range of 0-4% by weight was produced. Test pieces were produced by compacting at 589 MPa and sintering at 1120°C. The resulting impact energy values are apparent from Fig. 3. As shown therein, 0.3-3.5% by weight of Mo constitutes a useful range, whereas 0.5-2.5% by weight of Mo constitutes a preferred range.
Very likely, the results obtained are due to the fol-lowing. The addition of P entails that a liquid phase is obtained during sintering at a comparatively low tempera-Lure, resulting in a better distribution of P in the mate-rial. P diffuses into the iron particles, and, to some extent, austenite is transformed to ferrite, which faci-litates the diffusion of Mo. Both P and Mo are ferrite stabilisers, and the transformation to ferrite increases the self-diffusion of Fe. This gives an active sintering, resulting in shrinkage and round pores.
Suitably, P is present in the form of a phosphor com-pound, preferably iron phosphide, e.g. Fe3P.
The other alloying elements may be of a type not affecting the impact energy adversely, and common in pow-der metallurgy. As non-restrictive examples, mention may be made of Ni, W, Mn and Cr. Cu should not be used at all.
Claims (27)
1. An iron-based powder for producing impact-resis-tant components by powder compacting and sintering, which powder contains, in addition to Fe, 0.3-0.7% by weight of P, 0.3-3.5% by weight of Mo, and not more than 2% by weight of other alloying elements, optionally including a maximum of 0.1% by weight of C.
2. The powder of claim 1, wherein the amount of Mo is 0.5-2.5% by weight.
3. The powder of claim 1 or 2, wherein the amount of P is 0.35-0.65% by weight.
4. The powder of claim 1 or 2, wherein the amount of P is 0.4-0.6% by weight.
5. The powder of any one of claims 1 to 4, wherein the P is present in the form of iron phosphide.
6. The powder of any one of claims 1 to 4, wherein the P is in the form of Fe3P.
7. The powder of any one of claims 1 to 6, wherein the amount of other alloying elements does not exceed 1% by weight.
8. The powder of any one of claims 1 to 6, wherein the amount of other alloying elements does not exceed 0.5%
by weight.
by weight.
9. The powder of any one of claims 1 to 8, which does not contain more than 0.07% by weight of C.
10. A powder-metallurgically produced component, which, in addition to Fe, contains 0.3-0.7% by weight of P, 0.3-3.5% by weight of Mo, and not more than 2% by weight of other alloying elements, optionally including a maximum of 0.1% by weight of C.
11. The component of claim 10, wherein the amount of Mo is 0.5-2.5% by weight.
12. The component of claim 10 or 11, wherein the amount of P is 0.35-0.65% by weight.
13. The component of claim 10 or 11, wherein the amount of P is 0.4-0.6% by weight.
14. The component of any one of claims 10 to 13, wherein the P is present in the form of iron phosphide.
15. The component of any one of claims 10 to 13, wherein the P is in the form of Fe3P.
16. The component of any one of claims l0 to 15, wherein the amount of other alloying elements does not exceed 1% by weight.
17. The component of any one of claims 10 to 15, wherein the amount of other alloying elements does not exceed 0.5% by weight.
18. The component of any one of claims l0 to 17, which does not contain more than 0.07% by weight of C.
19. A method of powder-metallurgically producing impact-resistant steel components, which comprises using an iron-based powder which, in addition to Fe, contains 0.3-0.7% by weight of P, 0.3-3.5% by weight of Mo, and not more than 2% by weight, of other alloying elements, optionally including a maximum of 0.1% by weight of C; compacting the powder into the desired shape, and sintering the compact.
20. The method of claim 19, wherein the amount of Mo is 0.5-2.5% by weight.
21. The method of claim 19 or 20, wherein the amount of P is 0.35-0.65% by weight.
22. The method of claim 19 or 20, wherein the amount of P is 0.4-0.6% by weight.
23. The method of any one of claims 19 to 22, wherein the P is present in the form of iron phosphide.
24. The method of any one of claims 19 to 22, wherein the P is in the form of Fe3P.
25. The method of any one of claims 19 to 24, wherein the amount of other alloying elements does not exceed 1% by weight.
26. The method of any one of claims 19 to 24, wherein the amount of other alloying elements does not exceed 0.5%
by weight.
by weight.
27. The method of any one of claims 19 to 26, which does not contain more than 0.07% by weight of C.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| SE9002070A SE468583B (en) | 1990-06-11 | 1990-06-11 | YEAR-BASED POWDER, SHIPPING STEEL COMPONENTS OF THE POWDER AND WERE MADE TO MANUFACTURE THESE |
| SE9002070-2 | 1990-06-11 | ||
| PCT/SE1991/000404 WO1991019582A1 (en) | 1990-06-11 | 1991-06-07 | Iron-based powder, component produced therefrom, and method of producing the component |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CA2084679A1 CA2084679A1 (en) | 1991-12-12 |
| CA2084679C true CA2084679C (en) | 2003-04-01 |
Family
ID=20379728
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002084679A Expired - Fee Related CA2084679C (en) | 1990-06-11 | 1991-06-07 | Iron-based powder, component produced therefrom, and method of producing the component |
Country Status (10)
| Country | Link |
|---|---|
| EP (1) | EP0533812B1 (en) |
| JP (1) | JP3280377B2 (en) |
| KR (1) | KR100189234B1 (en) |
| AT (1) | ATE126461T1 (en) |
| BR (1) | BR9106546A (en) |
| CA (1) | CA2084679C (en) |
| DE (1) | DE69112214T2 (en) |
| ES (1) | ES2075961T3 (en) |
| SE (1) | SE468583B (en) |
| WO (1) | WO1991019582A1 (en) |
Families Citing this family (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE4331938A1 (en) * | 1993-09-16 | 1995-03-23 | Mannesmann Ag | Molybdenum-containing iron base powder |
| SE9401823D0 (en) * | 1994-05-27 | 1994-05-27 | Hoeganaes Ab | Nickel free iron powder |
| JP4616220B2 (en) * | 2006-07-18 | 2011-01-19 | Ｊｆｅテクノリサーチ株式会社 | Method for producing hollow metal body |
| JP4641010B2 (en) * | 2006-07-25 | 2011-03-02 | Ｊｆｅテクノリサーチ株式会社 | Hollow metal body |
| KR101912378B1 (en) * | 2010-12-30 | 2018-10-26 | 회가내스 아베 (피유비엘) | Iron based powders for powder injection molding |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| SE372293B (en) * | 1972-05-02 | 1974-12-16 | Hoeganaes Ab | |
| DE2613255C2 (en) * | 1976-03-27 | 1982-07-29 | Robert Bosch Gmbh, 7000 Stuttgart | Use of an iron-molybdenum-nickel sintered alloy with the addition of phosphorus for the production of high-strength workpieces |
-
1990
- 1990-06-11 SE SE9002070A patent/SE468583B/en not_active IP Right Cessation
-
1991
- 1991-06-07 ES ES91911997T patent/ES2075961T3/en not_active Expired - Lifetime
- 1991-06-07 JP JP51115991A patent/JP3280377B2/en not_active Expired - Fee Related
- 1991-06-07 CA CA002084679A patent/CA2084679C/en not_active Expired - Fee Related
- 1991-06-07 WO PCT/SE1991/000404 patent/WO1991019582A1/en active IP Right Grant
- 1991-06-07 DE DE69112214T patent/DE69112214T2/en not_active Expired - Fee Related
- 1991-06-07 BR BR919106546A patent/BR9106546A/en not_active IP Right Cessation
- 1991-06-07 EP EP91911997A patent/EP0533812B1/en not_active Expired - Lifetime
- 1991-06-07 AT AT91911997T patent/ATE126461T1/en not_active IP Right Cessation
-
1992
- 1992-12-08 KR KR1019920703140A patent/KR100189234B1/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| DE69112214T2 (en) | 1996-01-04 |
| JPH05507967A (en) | 1993-11-11 |
| SE468583B (en) | 1993-02-15 |
| EP0533812B1 (en) | 1995-08-16 |
| WO1991019582A1 (en) | 1991-12-26 |
| ATE126461T1 (en) | 1995-09-15 |
| KR100189234B1 (en) | 1999-06-01 |
| SE9002070D0 (en) | 1990-06-11 |
| KR930700243A (en) | 1993-03-13 |
| JP3280377B2 (en) | 2002-05-13 |
| BR9106546A (en) | 1993-06-01 |
| EP0533812A1 (en) | 1993-03-31 |
| DE69112214D1 (en) | 1995-09-21 |
| CA2084679A1 (en) | 1991-12-12 |
| ES2075961T3 (en) | 1995-10-16 |
| SE9002070L (en) | 1991-12-12 |
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