COST 507 - Repositório Aberto da Universidade do Porto

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The assessed excess Gibbs energy parameters in the liquid phase showed the existence of the miscibility gap. The excess Gibbs energy parameters in the Fcc_Al phase were not optimised. Table 2 shows the assessed parameters in the Cu-Li-Mg system. Table 2. The assessed excess Gibbs energy parameters in the Cu-Li-Mg system PHASE Liquid Liquid Liquid Bcc A2 Cu 32 Li 8 Mg 60 ( τ ) G(Laves_C15,Cu:Li;0) G(Laves_C15,Mg:Li;0) L(Laves_C15,Cu:Li,Mg;0) L Lo L, U Lo A,G G G Lo A 14191.577 14191.577 14191.577 1764.073 -9005.163 25000.000 30000.000 -55000.000 B*T - - - - - - - - The values in Table 2 were assessed using the temperatures of the phase transformations and verified with the enthalpy values obtained. The assessed parameter of the Bcc_A2 phase was probably too low because there was no significant solid solubility of copper both in the copper-lithium and the copper-magnesium systems. For the same reason the Hcp_A3 phase was considered as a binary phase. The optimisation of the Laves_C15 phase was carried out manually and yielded one interaction parameter as L(Laves_C15,Cu:Li,Mg;0) = -55000. 2 The Cu-Mg-Zr system 2.1 Introduction Baikov Institute of Metallurgy investigated the Cu-Mg-Zr system up to the amount of 50 wt.% Mg and 50 wt.% Zr using methods as light microscopy, X-ray phase analysis, local X-ray spectral analysis, and differential thermal analysis. One ternary phase was found in the system. According to local spectral analysis, the composition of the ternary phase was estimated as 50 at.% Cu, 25 at.% Mg, and 25 at.% Zr. Moreover, the phases from the binary systems as Cu-Mg and Cu-Zr could be distinguished in the studied alloys. The substantia] homogeneity ranges of some other phases were also established. The binary compounds Cu 5 Zr and Cu 5 iZr| 4 exist in the solution up to the amount of 3 at.% Mg. The phase Cu 2 Mg exists in the solution up to the amount of 2.5 at.% Zr. The phase equilibria in the solid state between ternary phase, binary phases, and Cu solid solution were determined. Two invariant phase reactions near Cu-rich corner were discovered, as well. Using the experimental results, the isothermal section of the phase diagram at 500 °C and the polythermal section in the composition of 90 wt.% Cu were constructed in this study [96Boc]. - 222
2.2 Assessment The optimisation of the Cu-Mg-Zr system was carried out using the data introduced in this work and from Kuznetsov [82Kuz]. The experimental data was stored in the file which was read to the optimisation module. The optimisation was carried out using the enthalpy parameters for the liquid and Fcc_Al phases. The entropy terms were excluded because there was no thermodynamic data available. Figure 3 shows the assessed phase diagram with the fixed amount of 93 wt.% copper including the experimental points N2 to N9. The assessed phase diagram agrees reasonably well with the experimental data except the sample N5 which showed minor solubility in the Fcc_Al + CU^ZT phase region. The calculated invariant temperature was 995.0 K which was lower than the experimental value of 1003 K. Table 3 shows the assessed parameters of the excess Gibbs energy in the system. The Laves_C15 was predicted as a binary phase due to the reason that there was no information available on the solubility of zirconium in this phase. Table 3. The assessed ternary excess Gibbs energy parameters in the Cu-Mg-Zr system PHASE Liquid Liquid Liquid Fcc_Al (Cu) L L° L 1 L·1 L° A +18168.2502 + 18168.2502 + 18168.2502 + 35752.6281 B*T - - 1300 QNZ ΦΝ3 X N4 + IS6 *N7 XN8 ©N9 0.02 0.04 0.0B WEIGHT FRACTION MG 0.08 Figure 3. The assessed Cu-Mg-Zr phase diagram with 93 wt.% Cu. 223 -
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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
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
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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
Page 221 and 222: ■ 888 24 HSM^«" 16—19 3 À I
Page 223 and 224: Thermodynamic Evaluations of the Al
Page 225: Fcc_Al aves_C15 ONU ΔΝ12 αΝ13
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
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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 and 260: Al-Mn-Si 873 K 0.90 Liquid 0.80 0.7
Page 261 and 262: A Thermochemical Assessment of Data
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
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European Commission EUR 18171 —CO
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NOTICE TO THE READER Information on
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