COST 507 - Repositório Aberto da Universidade do Porto

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An application of the data to the nitridation of TiAl alloys is in preparation. A key point is that the stable and metastable "stability diagrams" can be calculated, using the nitrogen pressure as a variable [97Sch]. 3.2 Ti-V-N system 3.2.1 Solidification of Ti-V-N alloys [97Zen2] Solidification of the TiVN alloys have been simulated under the equilibrium and Scheil conditions, respectively (Fig. 11 and 12 in Appendix IV). It has been shown that in the high temperature range, say above 2200°C, the solidification process of the alloys containing 5 at.% V is close to the equilibrium state, but it moved towards the Scheil mode in the temperature range below 2200°C. The calculated composition range of vanadium in the secondary α of the alloy 70TÌ5V25N (at.%) by the Scheil model is very close to the experimental one. But that of the β phase by Scheil model is larger and higher than the measured one, which indicates that the diffusion of vanadium in β can still proceed down to at least 1600°C. 3.2.2 Nitridation of Ti-V alloys [97Zen2] When a TiV alloy with higher than 50 at.% Ti is exposed to nitrogen at 1400°C, the nitrogen atoms are first dissolved in the β phase. After β is saturated with nitrogen, the α phase starts to form in the surface region. With the nitriding proceeding, the δ phase appears. This nitriding process is presented in Fig. 13 in Appendix IV as dashed line for the alloy of 80TÌ20V (at.%). Therefore, the outer layer on the samples nitrided for a long enough time is the Tirich fee phase (Ti,V)N|. x with a few percent of vanadium. The morphology of the reaction zone depends on the vanadium content of the alloy. The α layer can be avoided by increasing the vanadium content or by increasing the nitriding temperature. 3.3 Ti-Ni-N system The calculated phase diagrams are being used to analyze the denitrification and phase formation during the sintering process of TiNNi mixed powder compacts. It is found that the temperature at which the liquid phase appears strongly depends on the pressure. The thermodynamic dataset can be applied to design the sintering techniques for the TiNNi powder mixture. This work is in progress. References 79Fuk M. Fukuhara and H. Mitani: Nippon Kinzoku Gakkaishi 43 (1979) 169174. 82Wit M. Wittmer: J. Appi. Phys. 53 (1982) 10071012. 88
84Bey R. Beyers, R. Sinclair, and M. E. Thomas: J. Vac. Sci. Techno!. Β 2 (1984) 781-784. 91Bin S. Binder, W. Lengauer, and P. Ettmayer: J. Alloys & Compounds, 177 (1991) 119-127. 92Koy 93Jon 95Dup 95Fri 95E1S 96Zenl 96Zen2 97Dul 97Du2* 97Du3 97Sch K. Koyama, M. Morishita, K. Suzuki, S. Yagi: J. Jpn. Soc. Powder Powder Metall. 39 (1992) 823-829. S. Jonsson: "An assessment of the Ti-N system", in "Phase relations in quaternary hard materials", Ph.D Thesis, KTH Stockholm (1993). N. Dupin: "Thermodynamic evaluation of multicomponent nickel-base alloys", Ph.D Thesis, National Institute of Polytechnology of Grenoble, France (1995). Y. L. Friec, J. Bauer, and P. Rogl: "The N-Ni-Ti system", unpublished work (1995). M. H. El-Sayed, M. Naka, and J. C. Schuster: Proc. 5th Europe-Japan Bilateral Colloq. on Composite Materials, Corfu, Greece (1995) 329-333. K. Zeng and R. Schmid-Fetzer: "A critical assessment and thermodynamic modeling of the Ti-N system", Z. Metallkde., 87 (1996) 540-554. K. Zeng and R. Schmid-Fetzer: "Thermodynamic consideration of interfacial reaction between aluminum and titanium nitride", Proc. "Werkstoffwoche'96", DGM and DKG, (1996) in press. Y. Du, R. Schmid-Fetzer, H. Ohtani: "Thermodynamic assessment of the V-N system", Z. Metallkde. (1997) accepted. Y. Du, R. Wenzel and R. Schmid-Fetzer: "Calculation and measurement of the Al-V-N phase diagram", J. Chim. Phys. (1997), accepted. Y. Du, R. Wenzel and R. Schmid-Fetzer: "Thermodynamic analysis of reactions in the Al-N-Ta and Al-N-V systems", CALPHAD (1997) under review. R. Schmid-Fetzer and K. Zeng: "Nitridation of Ti-Al Alloys: A Thermodynamic Analysis", in preparation (1997). 97Zenl* K. Zeng and R. Schmid-Fetzer: "Thermodynamic modeling and applications of the Ti-Al-N phase diagram", in "Thermodynamics of Alloy Formation", eds. Y. A. Chang and F. Sommer, The Minerals, Metals and Materials Society (TMS), Warrendale, PA, 275-294 (1997). 97Zen2* K. Zeng and R. Schmid-Fetzer: "The Ti-V-N system: Thermodynamic assessment and applications", manuscript to be submitted (1997). 89
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European Commission COST European c
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European Commission COST European c
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Preface The Final Workshop of the C
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COST 507 STRUCTURE Measurement and
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GRl: Mirtee S.A., Volos Mr.P.Polati
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D9 Dll Fl GR2 II NI S3 SF1 "Thermop
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A Summary of the COST 507 Action an
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Aluminium-based systems Titanium-ba
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An Example using the COST 507 Datab
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Appendix COST 507: Some Key Meeting
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Al - 0.5 Fe, 1 Mg, 0.8 Mn, 0.2 Si (
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Fig 4 Aluminium beverage cans. The
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Fig 6 High pressure compressor vane
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INTRODUCTION All of us are aware of
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In the interaction with materials a
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There was a first warning more than
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Some time ago, the well-known physi
Page 42 and 43: Today there is a whole range of ins
Page 44 and 45: The dimension of this reservoir inc
Page 46 and 47: REFERENCES [ 1 ] G. Petzow, "Man, M
Page 48 and 49: Trends in Application of Materials
Page 50 and 51: Raw Materials The Cycle of Material
Page 52 and 53: i LÌ i.'»Af·· iù^ VV.V.X. iTTa
Page 54 and 55: 1600 OJ 1200 .« 1100 d 1000 900 Si
Page 57 and 58: Al Phase Relations in the Aluminium
Page 59 and 60: oundaries of the single phase regio
Page 61 and 62: Table 1 : Crystallographic Data of
Page 63 and 64: order to facilitate the evaluation
Page 65 and 66: (especially around 33 at% Mg) in or
Page 67 and 68: 3.System Ti-Sn-Al-N. The investigat
Page 69 and 70: 6) N.Durlu, U.Gruber, M.Pietzka, H.
Page 71 and 72: Summary of final report Directional
Page 73 and 74: calculate the thermodynamic mixing
Page 75 and 76: Introduction It is the aim of this
Page 77 and 78: Thermodynamic evaluations for high
Page 79 and 80: Figure 5 presents the calculated li
Page 81 and 82: There is a complete lack in the lit
Page 83 and 84: a.B5 ø.ia 0.15 0.20 0.25 0.30 0.35
Page 85 and 86: 700 [53Phi] 800 +[90Kuz21 ]iquld a
Page 87 and 88: Thermodynamic Assessments, Experime
Page 89 and 90: AIN and TiNi_ x is also given. Vari
Page 91: satisfied the three requirements of
Page 95 and 96: Material and Methods 2.1 Fabricatio
Page 97 and 98: 3.4 Electronmicroscopy (SEM) and X-
Page 99 and 100: Tab. 3: Density of the Ti20Albase
Page 101 and 102: Tab.5. continued TÌ20A1 5CulONi Ti
Page 103 and 104: Fig. 3: ESMA and Xray diffraction
Page 105 and 106: Fig.7: Wetting angle of Ti 15A1 lOC
Page 107 and 108: Thermophysical Properties of Light
Page 109 and 110: Tab.2 Chemical composition of terna
Page 111 and 112: 700 (AI)+AIFeS¡«_600 KS1275.1 l
Page 113 and 114: 4.2 Thermal conductivity of industr
Page 115 and 116: 4.3 AlSiZn alloys Electrical re
Page 117 and 118: 94Jar/Bra G.Jaroma-Weiland, R.Brand
Page 119 and 120: MgZn9 (C 14) and Mg2Zn u in the Al
Page 121 and 122: The three Laves phases were describ
Page 123 and 124: References [13Ege] G. Eger, Z. Meta
Page 125 and 126: 0.30 0.35 0.40 0.45 0.50 mole fract
Page 127 and 128: □ [48Koe] 600 500 400 0 0.1 0
Page 129 and 130: MggZn,, this work □ Single phase,
Page 131 and 132: Temperatures in °C 0.05 0.10 mole
Page 133 and 134: Table 2 : Alloy compositions Alloy
Page 135 and 136: All. Dy 50 Cpexp °C Cpadd Table 5
Page 137 and 138: Zn ¿Kl Si Fig. 2 : Position of the
Page 139 and 140: 22.5 ■■ 7.5 Temperature ICI Tem
Page 141 and 142: .to 2.5 "lõõ soo iÍOõ dOõ rtõ
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GR2 Differential Scanning Calorimet
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Time (x10 3 sec) Fig. 1. DSC Thermo
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solidification. It can be seen that
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4. Conclusions Differential scannin
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COST 507 - ROUND Π UNIT II SEZIONE
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[96Sac] The Rrich regions of the
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List of publications in the framewo
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2Contributions: oral or posters p
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1996 REPORT 2 s ' PART: ACTIVITY CA
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[96Sei] Excess Gibbs energy coeffic
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List of publications in the framewo
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Proc. :7 th Meeting on "Syntheses a
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2.1 Solid solubility measurements T
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eviews by Rivlin and Raynor [81 Riv
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inaires. Thesis, Universite Scienti
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Table 1. Review of the ternary phas
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L) Liq+bcc=FeSi+t_1 M) Liq+t 1=FeSi
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Extrapolations based on Ti-C-N S3 B
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value has been accepted in all thre
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with high precision whereas Jonsson
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only fit the hightemperature asym
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Jonsson combined his descriptions o
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Table II. Solubility product of TiC
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Ti-C, Z.Metallkd. 86 (1995) 5 319
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1000 1500 2000 2500 3000 Τ (K) Fig
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o Oí o 3 4 5 6 7
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M^øD^ O Kelley(1944) • Kelley an
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— cale, with Dumitrescu (1997) -
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€ gfc-π m-, .-π-, π-π .-saa J
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+graph 0 TiN 0.2 0.4 0.6 X TiC 0.8
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Binder et al (1992) TiN 1423 K ■
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0.08 600°C 700°C 800°C 900°C 10
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[59Sto]: Ä600°C □ 70D°C O8Q0°
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2000 Cale, with Saunders (1997) —
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An Experimental Investigation of th
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An Experimental Investigation of th
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211 -
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EXPERIMENTAL INVESTIGATION OF THE C
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Fig.1 SEM micrographs of CuMgZr
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■ 888 24 HSM^«" 16—19 3 À I
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Thermodynamic Evaluations of the Al
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Fcc_Al aves_C15 ONU ΔΝ12 αΝ13
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2.2 Assessment The optimisation of
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0.50 0.45 CulOZr7/ 0. 40 Or ^ 0.3
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References [71Kri] Kripyakevich, P.
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Kejun Zeng and Marko Hämäläinen,
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for detennining phase boundary and
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Table 2 Al-Fe-Mn results wt%Fe 0.5
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•00 Γ Ι I I I ~ LIQUID S^ 7iO
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the observed A2-B2 ordering. This p
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1473K Ahmed & Flower [94 Ahmi] 0.2
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900K Paruchuri & Massalski [91Par]
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BCC_B2#2 TI3RL TIPL BCC B2#2 TIRL
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0.2 0.3 0.4 0.5 X(LIQ,V) Figure 15
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1 Introduction and Overview of the
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at least 95% by Fe, possibly 99%, a
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8 References 43Phi H W L Phillips,
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1050 1000 Isopleth, Al - Si - 4 wt
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Al-Mn-Si 873 K 0.90 Liquid 0.80 0.7
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A Thermochemical Assessment of Data
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certainly due to the appearance of
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Materials Science Centre, November
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1400 Al-Mn Fig 2 Calculated partial
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1000 ι AlMn I Ι 950 Liquid E ω
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Al-Fe-Mn 843 K 0.90 0.80 0.70 0.60
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AlFeMn section at 2 wt% Mn co
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0.50 0.45 0.40-1 LU £ 0.35 LU 0.30
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European Commission EUR 18171 —CO
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NOTICE TO THE READER Information on
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