COST 507 - Repositório Aberto da Universidade do Porto

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phase to be 11.2 and 11 wt% respectively. These measurements were however conducted on samples where the cubic alpha-AlMnFeSi phase was also present which means that the hexagonal phase would have to contain an unnaturally high amount of Si compared to what is standard for the pure Al-Fe-Si system (without Mn). Corby [77Cor] found that the hexagonal phase contained 8.7 wt% Si. A complete review of the ternary phases included in the assessment is given in Table 1. The calculated enthalpy of formation at 298.15K for the alpha and beta phase is 23.4 and 18.2 kJ/mol, while the experimental values determined by Moquet [71Moq] are 23.23 and 20.04 kJ/mol respectively. The calculated diagrams generally reproduce the available experimental data well. However, emphasis has been placed on achieving a good fit in the aluminium rich corner, since this is where the bulk of the reliable data and the industrial interest is focused. It must be pointed out that even here there are still important points which have not been satisfactorily investigated such as the phase boundaries for Al 13 Fe 4 and the alpha-AlFeSi phase at higher Si contents, and the solubility range for the delta- AlFeSi phase. A redetermination of the invariant points and the enthalpy of formation of at least one of the ternary phases would also improve the assessment. A comparison between the calculated and experimental positions of the invariant points is shown in Table 2. As for the central part of the system, there is very little interest and thereby also little data in this region of the phase diagram. Two ternary compounds τ_1 and τ_3 are included in the diagram but their compositions and appearance in the diagram is uncertain. Later work has revealed the probable existence of several other phases [81 Zar], but they can not be included in the diagram before more information, such as melting points, enthalpies and equilibria with other phases have been investigated. 4 References [40Tak] H. P. Takeda and K. Mutuzaki, Tetso to Hagane, 1940, 26, 335. [50Phr G. Phragmen, J. Inst. Met., 1950, 77, 489. [51Pra] J. N. Pratt and G. V. Raynor, J. Inst. Metals, 1951, 79, 211. [54Arm] M. Armand, Congres International de l'Aluminium, 1954. [55BIa] P. J. Black, Philos. Mag., 1955, 46, 401. [59Phi] H. W. L. Phillips, Annotated Equilibrium Diagrams of some Aluminium Alloy Systems, Inst. Met., London, 1959. [67Mun] D. Munson, J. Inst. Met., 1967, 95, 217. [71Moq] J. L. Moq, Contribution a l'estimasjon des grandeurs thermodynamiques des composes intermetalliques et des entropies de fusion des eutectiques - 166 -
inaires. Thesis, Universite Scientifique et Medicale de Grenoble, 1971. [76Mon] L. F. Mondolfo, Aluminum Alloys: Structure and Properties Butterworths, London, 1976 [77Cor] R. N. Corby and P. J. Black, Acta. Crystallogr., 1977, 33B, 3468. C. J. Simensen, A. I. Spjelkavik, Fresenius Ζ. Analytische Chemie, [80Sim] 1980, 300, 177. [81Bou] F. R. Boutin, S. Dermarkar and B. Meyer, Proc. 7th Light Metals Congress, Leoben 1981, 212. [81Riv] V. G. Riviin and G. V. Raynor, Int. Met. Rev., 1981, 26, 133. [81Zar] O. S. Zarechnyuk, N. V. German, T. I. Yanson, R.M. Rykhal and Α. Α. Muravera, Some Phase Diagrams of Aluminium with Transition Metals, Rare Earth Elements and Silicon, Splav. Izd. Nauka, Moscow, 1981, 69. [84Don] A. L. Dons, Z. Metallkd., 1984, 75, 170. [84Sim] C. J. Simensen, P. Fartum and A. Andersen, Fresenius Ζ. Analytische Chemie, 1984, 319, 286-292. [86Sch] R. J. Schaefer, F. S. Biancaniello and J. W. Cahn, Scripta Met., 1986, 20, 1439. [87Gri] A. Griger, A. Lendvai, V. Stefaniay and T. TurmezeyJ. Mater. Sei. Forum, 1987, 13/14,331. [87Ste] V. Stefaniay, A. Griger and T. Turmezey, J. Mater. Sei., 1987,22, 539. [880sc] A. Oscarsson et al., Ζ. Metallkd., 1988, 79, 600. [89Bor] R. Borrely, P. Merle and D. Adenis, Light Metals 1989, EditonP. G. Campbell, 703. [92Gho] G. Ghosh, Ternary Alloys: Editors G. Petzow and G. Effenberg,VCH Verlagsgesellschaft, Weinheim, 1992. [93Sei] [93Kol] M. E. Seiersten, "An assessment of the Al-Fe and Al-Fe-Si systems", SINTEF report nr. STF28 F93051 June 1993. Ρ· Kolby, "The aluminium rich corner of the ternary Al-Mn-Si alloy system", SINTEF report nr. STF28 F93022 March 1993. [93Sim] C. J. Simensen, "Eutectic solidification of Aluminium-Silicon- Manganese alloys", SINTEF report nr. STF28 F93039 June 1993. - 167 -
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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
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Today there is a whole range of ins
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The dimension of this reservoir inc
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REFERENCES [ 1 ] G. Petzow, "Man, M
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Trends in Application of Materials
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Raw Materials The Cycle of Material
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i LÌ i.'»Af·· iù^ VV.V.X. iTTa
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1600 OJ 1200 .« 1100 d 1000 900 Si
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Al Phase Relations in the Aluminium
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oundaries of the single phase regio
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Table 1 : Crystallographic Data of
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order to facilitate the evaluation
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(especially around 33 at% Mg) in or
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3.System Ti-Sn-Al-N. The investigat
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6) N.Durlu, U.Gruber, M.Pietzka, H.
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Summary of final report Directional
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calculate the thermodynamic mixing
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Introduction It is the aim of this
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Thermodynamic evaluations for high
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Figure 5 presents the calculated li
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There is a complete lack in the lit
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a.B5 ø.ia 0.15 0.20 0.25 0.30 0.35
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700 [53Phi] 800 +[90Kuz21 ]iquld a
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Thermodynamic Assessments, Experime
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AIN and TiNi_ x is also given. Vari
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satisfied the three requirements of
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84Bey R. Beyers, R. Sinclair, and M
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Material and Methods 2.1 Fabricatio
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3.4 Electronmicroscopy (SEM) and X-
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Tab. 3: Density of the Ti20Albase
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Tab.5. continued TÌ20A1 5CulONi Ti
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Fig. 3: ESMA and Xray diffraction
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Fig.7: Wetting angle of Ti 15A1 lOC
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Thermophysical Properties of Light
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Tab.2 Chemical composition of terna
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700 (AI)+AIFeS¡«_600 KS1275.1 l
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4.2 Thermal conductivity of industr
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4.3 AlSiZn alloys Electrical re
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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
Page 143 and 144: GR2 Differential Scanning Calorimet
Page 145 and 146: Time (x10 3 sec) Fig. 1. DSC Thermo
Page 147 and 148: solidification. It can be seen that
Page 149 and 150: 4. Conclusions Differential scannin
Page 151 and 152: COST 507 - ROUND Π UNIT II SEZIONE
Page 153 and 154: [96Sac] The Rrich regions of the
Page 155 and 156: List of publications in the framewo
Page 157 and 158: 2Contributions: oral or posters p
Page 159 and 160: 1996 REPORT 2 s ' PART: ACTIVITY CA
Page 161 and 162: [96Sei] Excess Gibbs energy coeffic
Page 163 and 164: List of publications in the framewo
Page 165 and 166: Proc. :7 th Meeting on "Syntheses a
Page 167 and 168: 2.1 Solid solubility measurements T
Page 169: eviews by Rivlin and Raynor [81 Riv
Page 173 and 174: Table 1. Review of the ternary phas
Page 175 and 176: L) Liq+bcc=FeSi+t_1 M) Liq+t 1=FeSi
Page 177 and 178: Extrapolations based on Ti-C-N S3 B
Page 179 and 180: value has been accepted in all thre
Page 181 and 182: with high precision whereas Jonsson
Page 183 and 184: only fit the hightemperature asym
Page 185 and 186: Jonsson combined his descriptions o
Page 187 and 188: Table II. Solubility product of TiC
Page 189 and 190: Ti-C, Z.Metallkd. 86 (1995) 5 319
Page 191 and 192: 1000 1500 2000 2500 3000 Τ (K) Fig
Page 193 and 194: o Oí o 3 4 5 6 7
Page 195 and 196: M^øD^ O Kelley(1944) • Kelley an
Page 197 and 198: — cale, with Dumitrescu (1997) -
Page 199 and 200: € gfc-π m-, .-π-, π-π .-saa J
Page 201 and 202: +graph 0 TiN 0.2 0.4 0.6 X TiC 0.8
Page 203 and 204: Binder et al (1992) TiN 1423 K ■
Page 205 and 206: 0.08 600°C 700°C 800°C 900°C 10
Page 207 and 208: [59Sto]: Ä600°C □ 70D°C O8Q0°
Page 209 and 210: 2000 Cale, with Saunders (1997) —
Page 211 and 212: An Experimental Investigation of th
Page 213 and 214: An Experimental Investigation of th
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Page 217 and 218: EXPERIMENTAL INVESTIGATION OF THE C
Page 219 and 220: 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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