SE468583B - YEAR-BASED POWDER, SHIPPING STEEL COMPONENTS OF THE POWDER AND WERE MADE TO MANUFACTURE THESE - Google Patents
YEAR-BASED POWDER, SHIPPING STEEL COMPONENTS OF THE POWDER AND WERE MADE TO MANUFACTURE THESEInfo
- Publication number
- SE468583B SE468583B SE9002070A SE9002070A SE468583B SE 468583 B SE468583 B SE 468583B SE 9002070 A SE9002070 A SE 9002070A SE 9002070 A SE9002070 A SE 9002070A SE 468583 B SE468583 B SE 468583B
- Authority
- SE
- Sweden
- Prior art keywords
- weight
- powder
- sintering
- addition
- iron
- Prior art date
Links
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
Description
146 10 15 20 25 30 35 5 åšš 2 de rundare porerna till att öka slagsegheten. Alternativt kan en aktivare sintring uppnås genom tillsats av P, _ som också höjer hållfasthet och duktilitet samt rundar ; av porerna redan vid lägre sintringstemperaturer, dvs under 11so°c._ ' * Sammanfattningsvis kan en ökad slagseghet i sintrade material uppnås genom att anvisningsverkan från porerna reduceras. Detta kan åstadkommas genom smältfassintring, högtemperaturssintring, sintring av ett ferritiskt ma- terial, dubbelpressning och tillsättning av legerings- ämnen med en krympande effekt. 146 10 15 20 25 30 35 5 åšš 2 the rounder pores to increase the impact resistance. Alternatively, a more active sintering can be achieved by the addition of P, _ which also increases strength and ductility as well as rounds; of the pores already at lower sintering temperatures, ie below 110 ° C. In summary, an increased impact strength in sintered materials can be achieved by reducing the instruction effect from the pores. This can be achieved by melt phase sintering, high temperature sintering, sintering of a ferritic material, double pressing and addition of alloying elements with a shrinking effect.
Tillräcklig slagseghet uppnås dock i många fall först genom utnyttjande av en kombination av de ovan angivna åtgärderna och därmed krävs vanligen ett om- fattande och dyrbart processande vid användning av idag kända legeringssystem inom den pulvermetallurgiska tek- niken. Ändamålet med föreliggande uppfinning är därför att åstadkomma ett järnbaserat pulver, vilket förenklar processandet men ändå ger tillräckligt slagsega komponenter genom pulverpressning och sintring.However, in many cases sufficient impact resistance is achieved only by utilizing a combination of the above-mentioned measures, and thus extensive and expensive processing is usually required when using currently known alloy systems in powder metallurgical technology. The object of the present invention is therefore to provide an iron-based powder, which simplifies the processing but still provides sufficiently tough components by powder pressing and sintering.
Det är vidare ett önskemål att enkel pulverpressning kan tillämpas liksom sintring i en bandugn, dvs vid lägre temperaturer än ung ll50°C.It is further desired that simple powder pressing can be applied as well as sintering in a belt furnace, i.e. at lower temperatures than about 150 ° C.
Det har visat sig att detta ändamål kan uppnås medelst ett järnbaserat pulver, vilket förutom Fe inne- fattar Mo och P och där halten av övriga legeringsämnen, hålles på en låg nivå. Utmärkande för detta material är bl a att redan vid sintring under l150°C en slagseg- het uppnås som är högre än den hos idag kända pulver- metallurgiska material, vilka sintrats vid högre tem- peraturer. Materialet har god pressbarhet och förmåga r\ till stor krympning, så att det sintrade materialet får en hög densitet. Vid en och samma densitet har dess- utom materialet enligt uppfinningen en väsentligt högre slagseghet än idag kända pulvermetallurgiska material.It has been found that this object can be achieved by means of an iron-based powder, which in addition to Fe includes Mo and P and where the content of other alloying substances is kept at a low level. Characteristic of this material is, among other things, that even when sintering below 150 ° C, a impact property is achieved which is higher than that of powder metallurgical materials known today, which are sintered at higher temperatures. The material has good compressibility and the ability to shrink greatly, so that the sintered material has a high density. In addition, at one and the same density, the material according to the invention has a significantly higher impact resistance than powder metal metallurgical materials known today.
Den ingående mängden Mo skall ligga i intervallet 10 15 20 25 30 35 468 583 3 0,1-3,5 vikt-%, företrädesvis i intervallet 0,25-2,5 vikt-%. Den ingående mängden P skall vara 0,3¿0,7 vikt-%, företrädesvis 0,35-0,65 vikt-% och allra helst 0,4-0,6 vikt-%. Den ingående mängden av övriga legeringsämnen skall högst vara 0,5 vikt-%. Härvid kan C ingå med högst 0,1 vikt-%, företrädesvis högst 0,07 vikt-%.The constituent amount of Mo should be in the range of 0.1-3.5% by weight, preferably in the range of 0.25-2.5% by weight. The constituent amount of P should be 0.3 ° 0.7% by weight, preferably 0.35-0.65% by weight and most preferably 0.4-0.6% by weight. The constituent amount of the other alloying elements must not exceed 0.5% by weight. In this case, C can be present with a maximum of 0.1% by weight, preferably a maximum of 0.07% by weight.
Pulvret kan framställas genom tillverkning av ett baspulver, som består av rent Fe.eller Fe med Mo i fast lösning. Detta kan framställas som ett vattenatomiserat pulver eller som ett svamppulver. Baspulvret glödgas lämpligen i en reducerande atmosfär för sänkning av halten av föroreningsämnen. Därefter blandas pulvret med P respektive Mo och P och kompakteras till önskad form, varefter sintring sker vid en temperatur, som med fördel kan ligga under ll50°C.The powder can be prepared by making a base powder, which consists of pure Fe or Fe with Mo in solid solution. This can be prepared as a water atomized powder or as a sponge powder. The base powder is suitably annealed in a reducing atmosphere to lower the level of contaminants. The powder is then mixed with P and Mo and P, respectively, and compacted to the desired shape, after which sintering takes place at a temperature which can advantageously be below 115 ° C.
Exempel Ett baspulver av Fe med 1,5 vikt-% Mo framställdes genom vattenatomisering. Därefter tillsattes 0,5 vikt-% P. Provkroppar framställdes genom kompaktering vid tryck i området 4-8 ton/cmz. Provkropparna sintrades vid ll20°C under 30 minuter. Resulterande densiteter och slagsegheter framgår av den övre kurvan i fig 1, där kompakterings- trycket i ton/cm2 utgör parameter. Exempelvis erhölls en slagseghet på 180 J och en densitet av 7,46 g/cm3 vid ett kompakteringstryck på 8 ton/cmz.Example A base powder of Fe with 1.5% by weight of Mo was prepared by water atomization. Then 0.5% by weight of P. was added. Samples were prepared by compaction at a pressure in the range 4-8 tons / cm 2. The specimens were sintered at 120 ° C for 30 minutes. The resulting densities and impact strengths are shown in the upper curve in Fig. 1, where the compaction pressure in tonnes / cm2 is a parameter. For example, an impact strength of 180 J and a density of 7.46 g / cm 3 were obtained at a compaction pressure of 8 tons / cm 2.
En provkropp, som framställdes på samma sätt som ovan beskrivits men med uteslutande av Mo, fick en be- tydligt lägre slagseghet, vilket åskådliggöres av den undre kurvan i fig 1.A specimen, which was prepared in the same manner as described above but excluding Mo, had a significantly lower impact strength, as illustrated by the lower curve in Fig. 1.
Vid högtemperaturssintring krymper materialet mer, vilket ger högre densitet och därmed högre slagseghet.At high temperature sintering, the material shrinks more, which gives higher density and thus higher impact resistance.
Detta åskådliggöres av punkten A på den övre kurvan i fig. 1, som erhölls vid ett presstryck av 6 ton/cmz och sintring vid l250°C under 30 min.This is illustrated by point A on the upper curve in Fig. 1, which was obtained at a compression pressure of 6 tons / cm 2 and sintering at 220 ° C for 30 minutes.
Det skall noteras, att tillsatskombinationen P och Mo resulterar i en högre sintrad densitet jämfört med ett binärt system av Fe och P, även om detta dubbel- 468 583 10 15 20 25 30 4 pressas. Vid en och samma densitet ger dessutom materialet enligt uppfinningen en väsentligt högre slagseghet, vilket sannolikt är att hänföra till en mer aktiv sintring. samt en positiv växelverkan mellan Mo och P.It should be noted that the additive combination P and Mo results in a higher sintered density compared to a binary system of Fe and P, even if this is double-pressed. In addition, at one and the same density, the material according to the invention gives a significantly higher impact strength, which is likely to be attributed to a more active sintering. and a positive interaction between Mo and P.
Ett pulver enligt uppfinningen framställdes med ett innehåll av 1,5 vikt-% Mo samt varierande mängder P i intervallet 0-0,8 vikt-%. Provkroppar framställdes genom komprimering vid 589 MPa och sintring vid l120°C.A powder according to the invention was prepared with a content of 1.5% by weight of Mo and varying amounts of P in the range 0-0.8% by weight. Samples were prepared by compression at 589 MPa and sintering at 120 ° C.
Erhållen slagseghet i J framgår av fig 2. Såsom fig 2 visar uppnås ett maximivärde för P = 0,5 vikt-%, goda värden erhålles inom intervallet 0,3-0,7 vikt-% P, ännu bättre värden inom området 0,35-0,65 vikt-% P och de bästa värdena inom området 0,4-0,6 vikt-% P.The impact strength obtained in J is shown in Fig. 2. As Fig. 2 shows, a maximum value of P = 0.5% by weight is achieved, good values are obtained in the range 0.3-0.7% by weight P, even better values in the range 0, 35-0.65% by weight P and the best values in the range 0.4-0.6% by weight P.
På motsvarande sätt framställdes provkroppar med ett innehåll av 0,5 vikt-% P och ett varierande innehåll inom området 0-4 vikt-% Mo. Provkroppar framställdes genom pressning vid 589 MPa och dessa sintrades vid l120°C. Erhållna värden på slagsegheten framgår av fig 3. Denna figur visar ett användbart intervall på 0,1-3,5 vikt-% Mo och ett föredraget intervall på 0,25-2,5 vikt-% Mo.Correspondingly, specimens were prepared with a content of 0.5% by weight of P and a varying content in the range 0-4% by weight of Mo. Samples were prepared by pressing at 589 MPa and these were sintered at 120 ° C. The values obtained for the impact strength are shown in Fig. 3. This figure shows a useful range of 0.1-3.5% by weight Mo and a preferred range of 0.25-2.5% by weight Mo.
Det är troligt, att de uppnådda resultaten bl a beror på följande. Tillsatsen av P medför att en smält- fas uppnås under sintringen vid en relativt låg tempera- tur, vilket ger en bättre fördelning av P i materialet.It is probable that the results achieved are partly due to the following. The addition of P means that a melting phase is achieved during sintering at a relatively low temperature, which gives a better distribution of P in the material.
P diffunderar in i järnpartiklarna och en viss transfor- mering kommer att ske från austenit till ferrit. Diffu- sionen av Mo kommer därmed att underlättas. Både P och Mo är ferritstabilisatorer och den uppnådda transfor- meringen till ferrit höjer självdiffusionen av Fe. Detta ger en aktiv sintring med krympning och runda porer som följd.P diffuses into the iron particles and some transformation will take place from austenite to ferrite. The diffusion of Mo will thus be facilitated. Both P and Mo are ferrite stabilizers and the achieved transformation to ferrite increases the self-diffusion of Fe. This provides an active sintering with shrinkage and round pores as a result.
Lämpligen ingår P_i form av en fosforförening, företrädesvis järnfosfid, exempelvis Fe3P. 'xSuitably P 2 is in the form of a phosphorus compound, preferably iron phosphide, for example Fe 3 P. 'x
Claims (8)
Priority Applications (11)
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 |
DE69112214T DE69112214T2 (en) | 1990-06-11 | 1991-06-07 | IRON BASE POWDER, MIXTURE THEREOF AND PRODUCTION OF THIS MIXTURE. |
AT91911997T ATE126461T1 (en) | 1990-06-11 | 1991-06-07 | IRON BASE POWDER, MIXTURE THEREOF AND PRODUCTION OF THIS MIXTURE. |
ES91911997T ES2075961T3 (en) | 1990-06-11 | 1991-06-07 | IRON BASED POWDER, COMPONENT PRODUCED FROM THE SAME AND METHOD TO PRODUCE THE COMPONENT. |
EP91911997A EP0533812B1 (en) | 1990-06-11 | 1991-06-07 | Iron-based powder, component produced therefrom, and method of producing the component |
BR919106546A BR9106546A (en) | 1990-06-11 | 1991-06-07 | IRON BASE, COMPONENT PRODUCED FROM THE SAME, AND METHOD FOR PRODUCING THE COMPONENT |
CA002084679A CA2084679C (en) | 1990-06-11 | 1991-06-07 | Iron-based powder, component produced therefrom, and method of producing the component |
JP51115991A JP3280377B2 (en) | 1990-06-11 | 1991-06-07 | Iron-based powder, component manufactured therefrom, and method of manufacturing the component |
PCT/SE1991/000404 WO1991019582A1 (en) | 1990-06-11 | 1991-06-07 | Iron-based powder, component produced therefrom, and method of producing the component |
KR1019920703140A KR100189234B1 (en) | 1990-06-11 | 1992-12-08 | Iron-based powder, component produced therefrom, and method of producing the component |
US08/302,088 US5728238A (en) | 1990-06-11 | 1994-09-06 | Iron based powder, component produced therefrom and method of producing the component |
Applications Claiming Priority (1)
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 |
Publications (3)
Publication Number | Publication Date |
---|---|
SE9002070D0 SE9002070D0 (en) | 1990-06-11 |
SE9002070L SE9002070L (en) | 1991-12-12 |
SE468583B true SE468583B (en) | 1993-02-15 |
Family
ID=20379728
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
SE9002070A SE468583B (en) | 1990-06-11 | 1990-06-11 | YEAR-BASED POWDER, SHIPPING STEEL COMPONENTS OF THE POWDER AND WERE MADE TO MANUFACTURE THESE |
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 |
JP6040163B2 (en) * | 2010-12-30 | 2016-12-07 | ホガナス アクチボラグ (パブル) | Iron powder 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 BR BR919106546A patent/BR9106546A/en not_active IP Right Cessation
- 1991-06-07 CA CA002084679A patent/CA2084679C/en not_active Expired - Fee Related
- 1991-06-07 JP JP51115991A patent/JP3280377B2/en not_active Expired - Fee Related
- 1991-06-07 DE DE69112214T patent/DE69112214T2/en not_active Expired - Fee Related
- 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
- 1991-06-07 ES ES91911997T patent/ES2075961T3/en not_active Expired - Lifetime
- 1991-06-07 WO PCT/SE1991/000404 patent/WO1991019582A1/en active IP Right Grant
-
1992
- 1992-12-08 KR KR1019920703140A patent/KR100189234B1/en not_active IP Right Cessation
Also Published As
Publication number | Publication date |
---|---|
KR100189234B1 (en) | 1999-06-01 |
CA2084679C (en) | 2003-04-01 |
BR9106546A (en) | 1993-06-01 |
ATE126461T1 (en) | 1995-09-15 |
DE69112214T2 (en) | 1996-01-04 |
EP0533812B1 (en) | 1995-08-16 |
EP0533812A1 (en) | 1993-03-31 |
JPH05507967A (en) | 1993-11-11 |
KR930700243A (en) | 1993-03-13 |
SE9002070L (en) | 1991-12-12 |
DE69112214D1 (en) | 1995-09-21 |
CA2084679A1 (en) | 1991-12-12 |
SE9002070D0 (en) | 1990-06-11 |
JP3280377B2 (en) | 2002-05-13 |
ES2075961T3 (en) | 1995-10-16 |
WO1991019582A1 (en) | 1991-12-26 |
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