SE462837B - Method for producing a nitrogen-alloyed steel by powder metallurgy - Google Patents
Method for producing a nitrogen-alloyed steel by powder metallurgyInfo
- Publication number
- SE462837B SE462837B SE8802494A SE8802494A SE462837B SE 462837 B SE462837 B SE 462837B SE 8802494 A SE8802494 A SE 8802494A SE 8802494 A SE8802494 A SE 8802494A SE 462837 B SE462837 B SE 462837B
- Authority
- SE
- Sweden
- Prior art keywords
- nitrogen
- steel
- temperature
- capsule
- powder
- Prior art date
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 39
- 239000010959 steel Substances 0.000 title claims abstract description 39
- 238000004519 manufacturing process Methods 0.000 title description 3
- 238000004663 powder metallurgy Methods 0.000 title 1
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims abstract description 75
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 34
- 239000000843 powder Substances 0.000 claims abstract description 30
- 239000002775 capsule Substances 0.000 claims abstract description 18
- 229910001873 dinitrogen Inorganic materials 0.000 claims abstract description 11
- 238000000034 method Methods 0.000 claims abstract description 8
- 150000004767 nitrides Chemical class 0.000 claims abstract description 4
- 238000009792 diffusion process Methods 0.000 claims abstract 2
- 229910052799 carbon Inorganic materials 0.000 claims description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 6
- 239000007789 gas Substances 0.000 claims description 6
- 238000000265 homogenisation Methods 0.000 claims description 6
- 238000005121 nitriding Methods 0.000 claims description 5
- 229910001199 N alloy Inorganic materials 0.000 claims description 3
- 229910052720 vanadium Inorganic materials 0.000 claims description 3
- 229910052804 chromium Inorganic materials 0.000 claims description 2
- 229910052750 molybdenum Inorganic materials 0.000 claims description 2
- 239000000126 substance Substances 0.000 claims description 2
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims 1
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 claims 1
- 229910052782 aluminium Inorganic materials 0.000 claims 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims 1
- 229910052758 niobium Inorganic materials 0.000 claims 1
- 239000010955 niobium Substances 0.000 claims 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims 1
- 229910052715 tantalum Inorganic materials 0.000 claims 1
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 claims 1
- 229910052719 titanium Inorganic materials 0.000 claims 1
- 239000010936 titanium Substances 0.000 claims 1
- 229910052726 zirconium Inorganic materials 0.000 claims 1
- 238000003825 pressing Methods 0.000 abstract description 2
- MOYKHGMNXAOIAT-JGWLITMVSA-N isosorbide dinitrate Chemical compound [O-][N+](=O)O[C@H]1CO[C@@H]2[C@H](O[N+](=O)[O-])CO[C@@H]21 MOYKHGMNXAOIAT-JGWLITMVSA-N 0.000 abstract 1
- 238000007789 sealing Methods 0.000 abstract 1
- 238000006396 nitration reaction Methods 0.000 description 8
- 235000019589 hardness Nutrition 0.000 description 7
- 238000010586 diagram Methods 0.000 description 5
- 239000000203 mixture Substances 0.000 description 4
- 229910001566 austenite Inorganic materials 0.000 description 3
- 238000005242 forging Methods 0.000 description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 2
- 238000004220 aggregation Methods 0.000 description 2
- 230000002776 aggregation Effects 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- 238000005245 sintering Methods 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 229910000997 High-speed steel Inorganic materials 0.000 description 1
- 229910001315 Tool steel Inorganic materials 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000009689 gas atomisation Methods 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 230000005923 long-lasting effect Effects 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000161 steel melt Substances 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
Classifications
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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
- B22F3/12—Both compacting and sintering
- B22F3/14—Both compacting and sintering simultaneously
- B22F3/15—Hot isostatic pressing
-
- 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
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/16—Making metallic powder or suspensions thereof using chemical processes
-
- 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
-
- 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%
- C22C33/0285—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% with Cr, Co, or Ni having a minimum content higher than 5%
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- General Chemical & Material Sciences (AREA)
- Manufacturing & Machinery (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
- Powder Metallurgy (AREA)
Abstract
Description
462 '857 10 15 20 25 30 35 inte ett system av kommunicerande porer. Kvävgasen kan därför inte nå alla delar av pulvermassan, varigenom nitreringen blir ofullständig och inhomogen. Visserligen kan kvävet i viss grad fördelas genom en efterföljande homogeniseringsbehandling, men denna möjlighet är ändå begränsad. Om homogeniseringsbehandlingen är alltför långvarig eller utförs vid hög temperatur kan man nämligen inte undvika en betydande, skadlig kornförgrovning och/eller allvarlig karbidförgrovning. 462 '857 10 15 20 25 30 35 not a system of communicating pores. The nitrogen gas can therefore not reach all parts of the powder mass, whereby the nitration becomes incomplete and inhomogeneous. Although the nitrogen can to some extent be distributed through a subsequent homogenization treatment, this possibility is still limited. If the homogenization treatment is too long-lasting or is carried out at a high temperature, a significant, harmful grain aggregation and / or severe carbide aggregation cannot be avoided.
KORT REDOGÖRELSE FÖR UPPFINNINGEN Ändamålet med uppfinningen är att erbjuda ett förbättrat sätt att pulvermetallurgiskt framställa ett kvävelegerat stål, i synnerhet ett kvävelegerat verktygsstål, i synnerhet kallarbetsstål, eller snabb- stål. Dessa och andra syften kan uppnås därigenom att uppfinningen kännetecknas av vad som anges i de efterföljande patentkraven. Enligt uppfinningen satsar man sålunda ett gasatomiserat, sfäriskt stålpulver i en med gasinledningsrör försedd kapsel. Kapseln med innehåll värms till en temperatur mellan 700 och lOO0°C. Kvävgas med ett absolut tryck av 0.1-1.5 bar relativt det omgivande atmosfärstrycket inleds i kapseln vid nämnda temperatur genom gasinledningsröret. Härvid sker inte någon väsentlig sintring mellan pulverkornen. För att en.på detta stadium skadlig sintring skall ske behöver temperaturen vara betydligt högre och/eller ett pulverkornen sammanpressande tryck appliceras åtminstone då man såsom enligt uppfinningen utgår från ett sfäriskt stålpulver, vilket i sig är förhållandevis svårsintrat. Genom att genom val av sfäriskt stålpulver och genom att tillföra kvävet vid ett lågt tryck kommer pulverkroppen sålunda att bibehålla en i hög grad kommunicerande porositet under hela nitrerprocessen, så att kvävgasen kommer åt väsentligen alla delar av pulvermassan. Den inledda kvävgasen absorberas efter hand av stålpulvret genom indiffusion i stålet och genom att förenas med nitridbildare. På detta sätt fortsätter kvävgasinledningen i den takt kvävet absorberas av stålpulvret tills dess en viss, förutbestämd mängd kväve upptagits i stålet. Därefter avbryts kvävgasinledníngen och kapseln försluts hermetiskt.BRIEF SUMMARY OF THE INVENTION The object of the invention is to offer an improved way of powder metallurgically producing a nitrogen alloy steel, in particular a nitrogen alloy tool steel, in particular cold working steel, or high speed steel. These and other objects can be achieved in that the invention is characterized by what is stated in the appended claims. According to the invention, a gas-atomized, spherical steel powder is thus charged into a capsule provided with a gas inlet pipe. The capsule with contents is heated to a temperature between 700 and 100 ° C. Nitrogen gas with an absolute pressure of 0.1-1.5 bar relative to the ambient atmospheric pressure is introduced into the canister at said temperature through the gas inlet pipe. In this case, no significant sintering takes place between the powder grains. In order for a harmful sintering to take place at this stage, the temperature needs to be considerably higher and / or a compression pressure of the powder grains is applied at least when, as according to the invention, one starts from a spherical steel powder, which in itself is relatively difficult to sinter. By selecting spherical steel powder and by supplying the nitrogen at a low pressure, the powder body will thus maintain a highly communicating porosity throughout the nitriding process, so that the nitrogen gas accesses substantially all parts of the powder mass. The initiated nitrogen gas is gradually absorbed by the steel powder by indiffusion in the steel and by combining with nitride formers. In this way, the introduction of nitrogen gas continues at the rate at which the nitrogen is absorbed by the steel powder until a certain, predetermined amount of nitrogen has been taken up in the steel. Thereafter, the introduction of nitrogen is interrupted and the canister is hermetically sealed.
F: 10 15 20 25 30 35 462 857 Det finns ett jämviktssamband mellan å ena sidan halten kväve i fast lösning i det nitrerade pulvret och å andra sidan temperaturen och kvävets partialtryck i kammaren. Försök har vidare visat att det finns ett aproximativt samband mellan den inlösta kvävehalten för den undasökta legeringen i fråga och temperaturen vid en hålltid av en timma enligt följande: % N = 0.013 ' T - 9.1, då 725 < T(°C) < 800 Efter nitreringen upphettas kapseln och dess innehåll till en temperatur mellan 1050 och ll50°C för att väsentligen eliminera existerande kvävehaltsgradienter inuti stålet. Trots den höga porositeten hos pulvret under nitreringen kan man nämligen inte helt undvika vissa inhomogeniteter i det nitrerade pulvret. Dessa inhomogeniteter beror dels på att man i varje enskilt korn får en kvävehaltsgradient i riktning mellan ytan och kornets centrum, dels att man inte helt kan undvika att kvävehalten kommer att variera i olika delar av pulvret i kapseln. I synnerhet den första typen av kvävehaltdifferenser kan åtgärdas genom homogeniseringsbehandlingen, medan den andra typen av kvävehaltsskillnader är svårare att påverka genom homogeniseringsbehandling. Det senare slaget av inhomogeniteter är å andra sidan relativt obetydligt och innebär därför normalt inte något praktiskt problem. Efter homogeniseringen hetisostatpressas kapseln med innehåll vid högt tryck och hög temperatur till fullständig täthet enligt i och för sig känd teknik.F: 10 15 20 25 30 35 462 857 There is an equilibrium relationship between on the one hand the content of nitrogen in solid solution in the nitrated powder and on the other hand the temperature and the partial pressure of the nitrogen in the chamber. Experiments have further shown that there is an approximate relationship between the dissolved nitrogen content of the alloy in question and the temperature at a holding time of one hour as follows:% N = 0.013 'T - 9.1, then 725 <T (° C) <800 After nitration, the canister and its contents are heated to a temperature between 1050 and 115 ° C to substantially eliminate existing nitrogen content gradients inside the steel. Despite the high porosity of the powder during the nitration, certain inhomogeneities in the nitrated powder cannot be completely avoided. These inhomogeneities are partly due to the fact that in each individual grain you get a nitrogen content gradient in the direction between the surface and the center of the grain, and partly that you can not completely avoid that the nitrogen content will vary in different parts of the powder in the capsule. In particular, the first type of nitrogen content differences can be remedied by the homogenization treatment, while the second type of nitrogen content differences are more difficult to influence by homogenization treatment. The latter type of inhomogeneities, on the other hand, is relatively insignificant and therefore does not normally pose a practical problem. After homogenization, the capsule with high pressure and high temperature contents is hetistostatically pressed to complete density according to the technique known per se.
Ytterligare fördelar med samt kännetecken och aspekter på uppfinningen kommer att framgå av efterföljande utföringsexempel.Additional advantages and features and aspects of the invention will become apparent from the following working examples.
KORT FIGURBESKRIVNING I den följande beskrivningen av några utföringsexempel kommer att hänvisas till ritningsfiguren, som utgörs av ett diagram som visar hårdheten och restaustenithalten som funktion av austenitiserings- temperaturen vid härdning av fyra kallarbetsstål med varierande kol? och kvävehalter men i övrigt samma bassammansättning. 462 857 10 15 20 25 30 35 BESKRIVNING Av UTFÖRDA FöRsöK Vid försöken utgick man från två olika startsmältor. Vid framställning av de stål som i det följande benämnts nr 1 och nr 3 efter nitrering utgick man från en stålsmälta innehållande O.55% C och i övrigt följande nominella sammansättning: 1% Si, 8% Cr, l.6% Mo, 4% V och O.l% N, rest järn, föroreningar och accessoriska element i normala halter. I det andra fallet utgick man, för framställning av Stål nr 2 och nr 4, se nedan, från en stålsmälta med sammansättningen O.75% C och i övrigt samma nominella sammansättning som i förstnämnda fall. Av dessa smältor framställdes sfäriska stålpulver genom s k gasatomise- ring. Som atomiseringsgas användes kvävgas. Kvävehalterna hos det granulerade pulvret före fastfasnitreringen framgår av Tabell 1.BRIEF DESCRIPTION OF THE DRAWINGS In the following description of some embodiments, reference will be made to the drawing figure, which consists of a diagram showing the hardness and residual austenite content as a function of the austenitizing temperature when hardening four cold working steels with varying carbon? and nitrogen levels but otherwise the same base composition. 462 857 10 15 20 25 30 35 DESCRIPTION OF TESTS PERFORMED The experiments were based on two different starting melts. In the production of the steels hereinafter referred to as Nos. 1 and 3 after nitriding, a steel melt containing 0.55% C and the following nominal composition was used: 1% Si, 8% Cr, 1.6% Mo, 4 % V and Ol% N, residual iron, impurities and accessory elements at normal levels. In the second case, for the production of Steel Nos. 2 and 4, see below, a steel smelter with a composition of 0.75% C and otherwise the same nominal composition as in the former case was used. Spherical steel powders were produced from these melts by so-called gas atomization. Nitrogen gas was used as the atomizing gas. The nitrogen contents of the granulated powder before the solid phase nitration are shown in Table 1.
Av de sålunda framställda pulvren fylldes fyra kapslar, två kapslar med det förstnämnda pulvret och två med det andra, mer högkolhaltiga pulvret. Kapslarna med innehåll värmdes i en förvärmningsugn till ca 750°C. Därefter inleddes kvävgas i kapseln genom ett gasinledningsrör vid ett totaltryck av ca 1.5 bar. Kapseln var i övrigt tillsluten.Of the powders thus prepared, four capsules were filled, two capsules with the first-mentioned powder and two with the second, more high-carbon powder. The capsules with contents were heated in a preheating oven to about 750 ° C. Nitrogen gas was then introduced into the canister through a gas inlet pipe at a total pressure of about 1.5 bar. The capsule was otherwise closed.
Under nitreringen upprätthölls nämnda temperatur av ca 750°C. Nitre- ringstiderna för de fyra proverna framgår av Tabell 1. Kapseln för- slöts och det nitrerade pulvret homogeniserades genom att temperaturen höjdes till ca llOO°C. Därefter överfördes kapseln till en hetiso- statisk press, där pulvret kompakterades till fullständig täthet vid ett tryck av ca 1000 bar. De kompakterade ämnena smíddes därefter vid en smidestemperatur av ca ll50°C till klena stänger. De smidda stängerna härdades genom uppvärmning till varierande austenitiserings- temperaturer mellan 980 och lO80°C i 30 min, varefter de fick luft- svalna.During the nitration, said temperature of about 750 ° C was maintained. The nitration times for the four samples are shown in Table 1. The canister was sealed and the nitrated powder was homogenized by raising the temperature to about 1000 ° C. The capsule was then transferred to a hetisostatic press, where the powder was compacted to a complete density at a pressure of about 1000 bar. The compacted blanks were then forged at a forging temperature of about 115 ° C into thin bars. The forged rods were cured by heating to varying austenitization temperatures between 980 and 1080 ° C for 30 minutes, after which they were allowed to air cool.
Kol- och kvävehalter hos det gasatomiserade sfäriska pulvret före nitrering, hos pulvret efter nitrering, hos ämnet efter hetisostatisk pressning samt efter smidning framgår av Tabell 1.Carbon and nitrogen contents of the gas-atomized spherical powder before nitration, of the powder after nitration, of the substance after hetisostatic pressing and after forging are shown in Table 1.
Resultaten framgår även av diagrammen i ritningsfiguren. För varje stål l-4 finns två kurvor i diagrammet. Den övre kurvan representerar 10 15 20 462 857 hårdheten efter härdning, medan den undre kurvan representerar hård- heten efter härdning och dubbelanlöpning vid 200°C, 2h + 2h. Av diagrammet framgår tydligt att man med stål med en total halt av C + N av ca l.8%, varvid kvävehalten är ca 1%, kan uppnå hårdheter över 60 HRC redan från en austenitiseringstemperatur av 980°C, Stål nr 4. Även med Stål nr 2 och 3, som efter smidning innehåller en total C + N-halt av ca 1.3, resp l.4% kan uppnås hårdheter i storleksordningen 60 HRC eller däröver, om man härdar från en austenitiseríngstemperatur av åtminstone lO80°C. Med Stål nr l, som innehåller en total C + N-halt av ca 1%, varav ungefär hälften kväve, uppnås hårdheter av mellan 54.5 och 57.5 HRC.The results are also shown in the diagrams in the drawing figure. For each steel l-4 there are two curves in the diagram. The upper curve represents the hardness after curing, while the lower curve represents the hardness after curing and double annealing at 200 ° C, 2h + 2h. The diagram clearly shows that with steels with a total content of C + N of about 1.8%, with the nitrogen content being about 1%, hardnesses above 60 HRC can be achieved already from an austenitization temperature of 980 ° C, Steel no. 4. Also with steels Nos. 2 and 3, which after forging contain a total C + N content of about 1.3 and 1,4% respectively, hardnesses of the order of 60 HRC or above can be achieved, if hardened from an austenitizing temperature of at least 1080 ° C. With Steel No. 1, which contains a total C + N content of about 1%, of which about half is nitrogen, hardnesses of between 54.5 and 57.5 HRC are achieved.
Av diagrammet framgår även att restaustenithalten ökar ganska mycket med ökande austenitiseringstemperatur för Stål nr 4, medan restauste- nithalten påverkas i väsentligt mindre grad, eller inte alls, för Stål nr l-3, vilket återspeglar hårdhetens variation med austenitiserings- temperaturen.The diagram also shows that the residual austenite content increases quite a lot with increasing austenitizing temperature for Steel No. 4, while the residual austenite content is affected to a significantly lesser extent, or not at all, for Steel No. 1-3, which reflects the variation in hardness with the austenitizing temperature.
Tabell 1 Stål Före nitrering Nitrerings- Efter nítrering Efter HIP-ning Efter suidning* telperatur C N C+N T(°C) C N C+N C N C+N C N C+N 1 .55 0.1 .65 750 .55 .65 1 20 .55 49 1.04 .55 .47 1.02 2 75 0.1 65 750 .75 .65 1.#0 .73 .71 1.4# .73 .55 1.29 3 .55 0.1 .55 750 .55 .95 1.50 .55 .78 1.33 .55 .84 1.39 4 .75 0.1 .65 750 .75 .95 1.70 .73 1.07 1.80 .72 1.08 1.80 *Alternativt värmníng 1150°C, 1 h, luftsvalníngTable 1 Steel Before nitriding Nitrating- After nitriding After HIP-ning After welding * teleportation CN C + NT (° C) CN C + NCN C + NCN C + N 1 .55 0.1 .65 750 .55 .65 1 20 .55 49 1.04 .55 .47 1.02 2 75 0.1 65 750 .75 .65 1. # 0 .73 .71 1.4 # .73 .55 1.29 3 .55 0.1 .55 750 .55 .95 1.50 .55 .78 1.33 .55 .84 1.39 4 .75 0.1 .65 750 .75 .95 1.70 .73 1.07 1.80 .72 1.08 1.80 * Alternative heating 1150 ° C, 1 h, air cooling
Claims (5)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| SE8802494A SE462837B (en) | 1988-07-04 | 1988-07-04 | Method for producing a nitrogen-alloyed steel by powder metallurgy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| SE8802494A SE462837B (en) | 1988-07-04 | 1988-07-04 | Method for producing a nitrogen-alloyed steel by powder metallurgy |
Publications (3)
| Publication Number | Publication Date |
|---|---|
| SE8802494D0 SE8802494D0 (en) | 1988-07-04 |
| SE8802494L SE8802494L (en) | 1989-03-02 |
| SE462837B true SE462837B (en) | 1990-09-10 |
Family
ID=20372806
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| SE8802494A SE462837B (en) | 1988-07-04 | 1988-07-04 | Method for producing a nitrogen-alloyed steel by powder metallurgy |
Country Status (1)
| Country | Link |
|---|---|
| SE (1) | SE462837B (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| AT411580B (en) * | 2001-04-11 | 2004-03-25 | Boehler Edelstahl | METHOD FOR THE POWDER METALLURGICAL PRODUCTION OF OBJECTS |
| CN110014144A (en) * | 2019-02-20 | 2019-07-16 | 益阳市再超粉末冶金有限公司 | A kind of powder metallurgy antifriction material for automobile gearbox |
| US11007571B2 (en) | 2018-02-27 | 2021-05-18 | Rolls-Royce Plc | Method of manufacturing an austenitic iron alloy |
-
1988
- 1988-07-04 SE SE8802494A patent/SE462837B/en not_active IP Right Cessation
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| AT411580B (en) * | 2001-04-11 | 2004-03-25 | Boehler Edelstahl | METHOD FOR THE POWDER METALLURGICAL PRODUCTION OF OBJECTS |
| US11007571B2 (en) | 2018-02-27 | 2021-05-18 | Rolls-Royce Plc | Method of manufacturing an austenitic iron alloy |
| CN110014144A (en) * | 2019-02-20 | 2019-07-16 | 益阳市再超粉末冶金有限公司 | A kind of powder metallurgy antifriction material for automobile gearbox |
Also Published As
| Publication number | Publication date |
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| SE8802494L (en) | 1989-03-02 |
| SE8802494D0 (en) | 1988-07-04 |
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