Sinterizazio-atmosferaren eragina M graduko (ASP 30 ... - Euskara
Sinterizazio-atmosferaren eragina M graduko (ASP 30 ... - Euskara Sinterizazio-atmosferaren eragina M graduko (ASP 30 ... - Euskara
INTRODUCTION Work carried out in the last two decades on the sintering of high speed steel powders has allowed obtaining high density components with near net shapes . One of these routes is direct sintering, consisting of cold compaction of annealed water atomized powders and subsequent vacuum sintering to full density . This technique has been succesfully applied to T1(1), M2(1), T6(2), T42(3,4), T15(5) and M42(6) . In many cases to compensate for the loss of carbon due to its reaction with the oxygen present at the surface of the powders, some elemental carbon is added to the prealloyed powders before sintering(7-9) . Such addition results also in an acceleration of the sintering kinetics, explained by some authors by the effect of carbon reducing the steel solidus temperature (10) . More recently Wright (11) has proposed that the sintering mechanism in this type of steels is "supersolidus" . Previous work in CEIT has proposed an alternative route to the vacuum sintering, reaching theoretical densities by sintering in a flowing atmosphere of N 2-H 2-CH 4 . Work has been performed on M2(12), T15(13), T42(14), T6(15) and M42(16) . In two recent papers, one on T42(17) and the other on T15 and M2(18), a consistent decrease in the optimum atmosphere sintering temperature compared with vacuum for T grades has been reported, but the optimum atmosphere sintering temperature was slightly higher than that found during vacuum sintering for M2(18) . During atmosphere sintering a finer microstucture is normally also produced due to the substitution of massive MC carbides by MX fine and coarsening resistent carbonitrides . It is also reported that for the T grades oversintering by up to 40K in the gas atmosphere does not significantly modify the microstucture and continuous films of eutectic are not observed, but a continuous film of eutectic is observed even for the optimum atmosphere sintering temperature for M2 . 2
Fracture toughness tests performed on these T grade steels gas sintered(16,19-21), quenched and tempered have shown K, 0 values similar to vacuum sintered high speed steels . In the present work the vacuum sintering behaviours of two Px30 steels, one of them rich in sulphur(Px30S free-machining grade), are compared with sintering in the gas mixture N 2-H2CH 4 to see if sintering in an atmosphere rich in nitrogen has also effect on M grade high speed steels, other than M2 . The effect of an addition of 0 .2% elemental carbon to these two steels is also studied . After sintering, the carbon, oxygen and nitrogen content are analyzed together with the microstructure characterized by the austenite content, initial grain size and the composition, size and volume fraction of the primary carbides . Sintering in the gas atmosphere will allow cost saving due to the low temperature sintering, and improvement in microstructure, mechanical properties and performance in service and offers the prospect of significant competitive advantage to manufacturers of tool and wear parts . EXPERIMENTAL PROCEDURE Vacuum annealed, water atomized Px30 and Px30S powders were bought from Powdrex Limited, Tonbridge, U .K. The -ccr_nposition_and sieve analysis of the powders provided by the . . . manufacturer are given in Tables I and II respectively . Additions of 0 .2 weight % of elemental carbon in the form of graphite, 15 µm mean size, were made and appropiate amounts of dry powders and graphite mixed for a period of 4 hours . Compacts of 16 mm diameter, weighing 4 g were cold compacted uniaxially at a pressure of 500 MPa, the walls being lubricated . This resulted in a green density of 5 .4x 10 3 and 5 .6x 10 3 kgm -3 for the Px30 and Px30S steels respectively. These values are equivalent to 65.9% TD for Px30 and 68 .3% TD for Px30S . The compacts were sintered either in a flowing atmosphere composed of 90% volume N29%H 2-1 %CH 4 or in vacuum . In this second case the vacuum was 3
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- Page 314 and 315: Figure 1 Microstructure of T42 + 0.
- Page 316 and 317: Figure 3 Microstructure of T15 (1 .
- Page 318 and 319: . . . 4 --s-- r a- 10 im Figure 5 M
- Page 320 and 321: TABLE V Chemical analysis of M 23 C
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- Page 336 and 337: etter than 5 Pa during the sinterin
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- Page 354 and 355: TABLE VII Chemical composition of C
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- 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
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- Page 375 and 376: DISCUSSION Densification Kinetics .
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- Page 383 and 384: CONDICION I C N (%owt) (%wt) O (%wt
Fracture toughness tests performed on these T grade steels gas<br />
sintered(16,19-21), quenched and tempered have shown K, 0 values similar to<br />
vacuum sintered high speed steels .<br />
In the present work the vacuum sintering behaviours of two Px<strong>30</strong><br />
steels, one of them rich in sulphur(Px<strong>30</strong>S free-machining grade), are compared with<br />
sintering in the gas mixture N 2-H2CH 4 to see if sintering in an atmosphere rich in<br />
nitrogen has also effect on M grade high speed steels, other than M2 . The effect of<br />
an addition of 0 .2% elemental carbon to these two steels is also studied . After<br />
sintering, the carbon, oxygen and nitrogen content are analyzed together with the<br />
microstructure characterized by the austenite content, initial grain size and the<br />
composition, size and volume fraction of the primary carbides . Sintering in the gas<br />
atmosphere will allow cost saving due to the low temperature sintering, and<br />
improvement in microstructure, mechanical properties and performance in service<br />
and offers the prospect of significant competitive advantage to manufacturers of tool<br />
and wear parts .<br />
EXPERIMENTAL PROCEDURE<br />
Vacuum annealed, water atomized Px<strong>30</strong> and Px<strong>30</strong>S powders were<br />
bought from Powdrex Limited, Tonbridge, U .K. The -ccr_nposition_and sieve analysis<br />
of the powders provided by the . . . manufacturer are given in Tables I and II<br />
respectively . Additions of 0 .2 weight % of elemental carbon in the form of graphite,<br />
15 µm mean size, were made and appropiate amounts of dry powders and graphite<br />
mixed for a period of 4 hours .<br />
Compacts of 16 mm diameter, weighing 4 g were cold compacted<br />
uniaxially at a pressure of 500 MPa, the walls being lubricated . This resulted in a<br />
green density of 5 .4x 10 3 and 5 .6x 10 3 kgm -3 for the Px<strong>30</strong> and Px<strong>30</strong>S steels<br />
respectively. These values are equivalent to 65.9% TD for Px<strong>30</strong> and 68 .3% TD for<br />
Px<strong>30</strong>S . The compacts were sintered either in a flowing atmosphere composed of<br />
90% volume N29%H 2-1 %CH 4 or in vacuum . In this second case the vacuum was<br />
3