COST 507 - Repositório Aberto da Universidade do Porto

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Τ=823 Κ 1 r 94Kol/S¡g Δ fee + cubic alpha + ΑΙ6Μη □ fcc + cubic alpha O fcc + cubic alpha + Si 0.5 1.0 Wt % Si Fig 5 Calculated partial isothermal section for the ΑΙrich corner of the AlFeMn system at 823 K, showing the fcc solvus. Experimental data of Kolby et al [94Kol/Sig] are superimposed. 256
A Thermochemical Assessment of Data for the Al-rich Corner of the Al-Fe-Mn System, and a Revision of Data for the Al-Mn System Abstract Åke Jansson' and Tim G Chart* "Royal Institute of Technology, Stockholm, Sweden *Chart Associates, Ashford, Middlesex, UK This research forms part of the COST 507 programme on the Al-Fe-Mg-Mn-Si system (Leading System 1). It includes a revision of data for the binary Al-Mn system, based upon the original COST 507 assessment for this system [92Jan, 94Ans] and an optimisation of data for the Al-rich corner of the Al-Fe-Mn ternary system, which in addition to the available published data, incorporates the results of experimental measurements carried out during the Action by a combination of Alean International Ltd (Banbury Laboratory), Katholieke Universiteit Leuven, Pechiney, SINTEF, Universität Wien and University of Manchester/UMIST; these experiments specifically performed to provide missing data, as described in other papers of the proceedings of the COST 507 Final Workshop, eg [97Rob/Hay]. The overall system currently under study is the Al-Fe-Mg-Mn-Si system. The phase relationships in the base Al-Fe-Mn-Si system itself are very complex and not wellestablished. In particular, during Leading System 1 meetings held on the quinary system and its constituent sub-systems, it became clear that the phase diagram data for some of these key sub-systems, largely based on the early work of Phillips [43Phi] may be subject to considerable experimental uncertainty, especially data for the Al-Mn binary system and the Al-Fe-Mn and Al-Mn-Si ternary systems, due, eg, to difficulties of nucleation, the presence of metastable phases and the effects of impurities. The results of the assessments are summarised. The experimental phase equilibrium studies carried out in combination by the above groups have proven to be essential to the project. It is clear, however, that some further careful experimentation is required. 257
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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
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MgZn9 (C 14) and Mg2Zn u in the Al
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The three Laves phases were describ
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References [13Ege] G. Eger, Z. Meta
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0.30 0.35 0.40 0.45 0.50 mole fract
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□ [48Koe] 600 500 400 0 0.1 0
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MggZn,, this work □ Single phase,
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Temperatures in °C 0.05 0.10 mole
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Table 2 : Alloy compositions Alloy
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All. Dy 50 Cpexp °C Cpadd Table 5
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Zn ¿Kl Si Fig. 2 : Position of the
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22.5 ■■ 7.5 Temperature ICI Tem
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.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°
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
Page 221 and 222: ■ 888 24 HSM^«" 16—19 3 À I
Page 223 and 224: Thermodynamic Evaluations of the Al
Page 225 and 226: Fcc_Al aves_C15 ONU ΔΝ12 αΝ13
Page 227 and 228: 2.2 Assessment The optimisation of
Page 229 and 230: 0.50 0.45 CulOZr7/ 0. 40 Or ^ 0.3
Page 231 and 232: References [71Kri] Kripyakevich, P.
Page 233 and 234: Kejun Zeng and Marko Hämäläinen,
Page 235 and 236: for detennining phase boundary and
Page 237 and 238: Table 2 Al-Fe-Mn results wt%Fe 0.5
Page 239 and 240: •00 Γ Ι I I I ~ LIQUID S^ 7iO
Page 241 and 242: the observed A2-B2 ordering. This p
Page 243 and 244: 1473K Ahmed & Flower [94 Ahmi] 0.2
Page 245 and 246: 900K Paruchuri & Massalski [91Par]
Page 247 and 248: BCC_B2#2 TI3RL TIPL BCC B2#2 TIRL
Page 249 and 250: 0.2 0.3 0.4 0.5 X(LIQ,V) Figure 15
Page 251 and 252: 1 Introduction and Overview of the
Page 253 and 254: at least 95% by Fe, possibly 99%, a
Page 255 and 256: 8 References 43Phi H W L Phillips,
Page 257 and 258: 1050 1000 Isopleth, Al - Si - 4 wt
Page 259: Al-Mn-Si 873 K 0.90 Liquid 0.80 0.7
Page 263 and 264: certainly due to the appearance of
Page 265 and 266: Materials Science Centre, November
Page 267 and 268: 1400 Al-Mn Fig 2 Calculated partial
Page 269 and 270: 1000 ι AlMn I Ι 950 Liquid E ω
Page 271 and 272: Al-Fe-Mn 843 K 0.90 0.80 0.70 0.60
Page 273 and 274: AlFeMn section at 2 wt% Mn co
Page 275: 0.50 0.45 0.40-1 LU £ 0.35 LU 0.30
Page 279: European Commission EUR 18171 —CO
Page 284: NOTICE TO THE READER Information on
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COST 507 - Repositório Aberto da Universidade do Porto

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