Sinterizazio-atmosferaren eragina M graduko (ASP 30 ... - Euskara
Sinterizazio-atmosferaren eragina M graduko (ASP 30 ... - Euskara Sinterizazio-atmosferaren eragina M graduko (ASP 30 ... - Euskara
The reason for the need of higher tempering temperatures to reach peak hardness in these steels is the high amount of nitrogen picked-up during their sintering in the N2-H2-CH4 atmosphere used . As pointed out before, this has as consequence the transformation of MC carbides into MX carbonitrides, leaving free some amount of carbon and producing an appreciable increase in the amount of retained austenite . The elimination of a much higher amount of -retained austenite, also more stable, requires higher tempering temperatures for conditioning it to be transformed into martensite in the cooling following tempering . It seems reasonable to assume that the higher the excess of carbon equivalent -the larger the amount of retained austenite, as shown in Fig .14- and the higher the tempering temperature required to transform it . Table V shows the excess in carbon equivalent, defined previously in Ec .2, the excess in stoichiometric carbon equivalent (SCE)(20), SCE = %C+12/14%N -[0 .033(%W)+0 .063(%Mo)+0 .176(%V)+0 .060(%Cr)] Ec .3 and the ratio between carbide formers and carbon (20), R = E atomic % carbide formers/atomic % (C+N) Ec .4 for the steels investigated in the present work and the standard grades . It is clearly apparent that by sintering in the gas atmosphere important carbon equivalent excesses and low R values are obtained in comparison with standard grades . The experimental results found in the present work indicate that for excesses in carbon equivalent around 0 .7 for Ec. and around 0 .5 for Ec. an increase in the peak hardness can be obtained by appropriated tempering, but when these excesses are very_ high,_ ie__for_ T15 steel (ACeq=0 .92 and ASCE = 0 .85) the supersaturation in carbon is so high that for tempering at high temperatures a coarse (Fe,Cr)7C3 is precipitated as shown in Fig . 16 and no additional increase in peak hardness is produced . Fracture Toughness . In Fig . 13 has been shown that a clear decrease of toughness occurs with increasing hardness . The fact that the results for the three steel could be reasonably fitted to a single straight line, indicates that fracture toughness is only related to hardness being independent of the steel composition and of the amount of
primary carbides present in the microstructure . This correlation has been also found by other authors (15) and have been interpreted in terms of fracture toughness mainly related to the matrix properties and not to the amount, size and morphology of the primary carbides . It is clearly apparent that the lower hardness values and therefore the higher fracture toughness values are obtained for atmosphere sintered specimens . This is a consequence of the increasing in the amount of retained austenite produced by atmosphere sintered specimens, due to the release of carbon by transforming the MC carbides to MX carbonitrides . The actual values of fracture toughness are higher than those found for conventional wrought high speed steel and similar to other values reported for vacuum sintered steels (15) CONCLUSIONS 1 . Sintering high speed steel powders in a gas atmosphere allows to obtain full density at lower temperatures than in vacuum sintering . The decrease in the optimum sintering temperature, being higher the higher the amount of vanadium in the steel . 2 . The "sintering gate" or the amount of oversintering without the formation or a continuous deletorius layer of eutectic carbide is also elarged by gas atmosphere sintering . 3 . By sintering in the nitrogen rich atmosphere massive MC carbides are replaced by fine MX carbonitrides, very resistant to coarsening . 4 . The presence of these fine and very stable MX carbonitrides inhibits the fast grain coarsening observed in vacuum sintering for oversintering temperatures and the austenite grain size is fine even for important oversintering when sintering in the gas atmosphere . 5 . The as-quenched microstructures in gas sintered high speed steels contain higher amounts of retained austenite than the same steels vacuum sintered . This allows the obtention, by simple tempering, of a broad variety of mechanical properties by the an adequate combination of hardness and toughness . 6. The tempering peak hardness occurs in atmosphere sintered steels at higher temperatures than in vacuum sintered steels . When the excess of carbon equivalent
- Page 328 and 329: The presence of these MX carbonitri
- Page 332 and 333: Publishing & Editorial The Institut
- Page 334 and 335: INTRODUCTION Work carried out in th
- Page 336 and 337: etter than 5 Pa during the sinterin
- Page 338 and 339: gas atmosphere (see Table IV for qu
- Page 340 and 341: - Needle type : observed only at hi
- Page 342 and 343: -1o- (18) . These values would give
- Page 344 and 345: Chemical composition of primary car
- Page 346 and 347: CONCLUSIONS 1 . Addition of free ca
- Page 348 and 349: Vasco, 1987, Bilbao, España . 13 .
- Page 350 and 351: TABLE I Chemical analysis of as-rec
- Page 352 and 353: TABLE IV Austenite grain size and p
- Page 354 and 355: TABLE VII Chemical composition of C
- Page 356 and 357: 8 .5 8 `/ U) 7 c o 6 .5 6 5 .5 1 1
- Page 358 and 359: Fig . 3 : Microstructure at the opt
- Page 360 and 361: L Ú y i3 70 60 30 - L 2 0 r- i Q L
- Page 362 and 363: Frecuency (%) 100 90 - 80 70 - 60 -
- Page 364 and 365: Frecuency (%) 100 90 - 80 - 70 - 60
- Page 366 and 367: Fig. 8 a) Eutectic type carbides .
- Page 369 and 370: March 10, 1992 Mr . J . J . Urcola
- Page 371 and 372: INTRODUCTION Work carried out in th
- Page 373 and 374: sintered is observed in Table II .
- Page 375 and 376: DISCUSSION Densification Kinetics .
- Page 377: particle size smaller than 1 µm, w
- Page 381 and 382: REFERENCES : 1 . F .L. Jaegger and
- Page 383 and 384: CONDICION I C N (%owt) (%wt) O (%wt
- Page 385 and 386: CONDICION Temperatura de sintetizad
- Page 387 and 388: 1 a v~ 00 v~ N 0o N ( £ m3/2) kLIS
- Page 389 and 390: u ( £ m0/ 2 ) xi ISNEIQ J 0 N M r-
- Page 391 and 392: Fig . 5 . Microstructure of T15 spe
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- Page 397 and 398: Q O x á á á 0 0 0 0 0 0 0 VI) L
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- Page 401 and 402: Ar, W X -r (3) a IU"EldWRI 0 M X A4
The reason for the need of higher tempering temperatures to reach<br />
peak hardness in these steels is the high amount of nitrogen picked-up during their<br />
sintering in the N2-H2-CH4 atmosphere used . As pointed out before, this has as<br />
consequence the transformation of MC carbides into MX carbonitrides, leaving free<br />
some amount of carbon and producing an appreciable increase in the amount of<br />
retained austenite . The elimination of a much higher amount of -retained austenite,<br />
also more stable, requires higher tempering temperatures for conditioning it to be<br />
transformed into martensite in the cooling following tempering . It seems reasonable<br />
to assume that the higher the excess of carbon equivalent -the larger the amount of<br />
retained austenite, as shown in Fig .14- and the higher the tempering temperature<br />
required to transform it . Table V shows the excess in carbon equivalent, defined<br />
previously in Ec .2, the excess in stoichiometric carbon equivalent (SCE)(20),<br />
SCE = %C+12/14%N -[0 .033(%W)+0 .063(%Mo)+0 .176(%V)+0 .060(%Cr)] Ec .3<br />
and the ratio between carbide formers and carbon (20),<br />
R = E atomic % carbide formers/atomic % (C+N) Ec .4<br />
for the steels investigated in the present work and the standard grades . It is clearly<br />
apparent that by sintering in the gas atmosphere important carbon equivalent<br />
excesses and low R values are obtained in comparison with standard grades . The<br />
experimental results found in the present work indicate that for excesses in carbon<br />
equivalent around 0 .7 for Ec. and around 0 .5 for Ec. an increase in the peak<br />
hardness can be obtained by appropriated tempering, but when these excesses are<br />
very_ high,_ ie__for_ T15 steel (ACeq=0 .92 and ASCE = 0 .85) the supersaturation in<br />
carbon is so high that for tempering at high temperatures a coarse (Fe,Cr)7C3 is<br />
precipitated as shown in Fig . 16 and no additional increase in peak hardness is<br />
produced .<br />
Fracture Toughness .<br />
In Fig . 13 has been shown that a clear decrease of toughness occurs<br />
with increasing hardness . The fact that the results for the three steel could be<br />
reasonably fitted to a single straight line, indicates that fracture toughness is only<br />
related to hardness being independent of the steel composition and of the amount of