COST 507 - Repositório Aberto da Universidade do Porto

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1 Introduction During the last two years new experimental measurements on the Al-Mn and Al-Fe-Mn systems have been carried out at Alean International Ltd (Banbury Laboratory) by Thornton and Evans, and at University of Manchester/UMIST by Hayes et al, specifically to elucidate the problems, following recommendations made COST 507 progress meetings. Work carried out as part of the COST 507 Action and under the present project, together with supplementary work has incorporated these new data, and (a) has provided a revised and improved dataset for the Al-Mn binary system which is consistent with our current understanding of experimental data for this system, and (b) has provided an updated dataset for the Al-Fe-Mn ternary system which is considered very satisfactory for present purposes. The effort has been considerable, and the problems, now largely resolved, have understandably delayed the development of the Al-Fe-Mg-Mn-Si database, also the addition of Cu. Although further work is required on the Al-Mn-Si system, which suffers related experimental uncertainties, especially the data of [43Phi], the current situation is good, very much improved compared with that of a year ago. The results of experimental measurements on the Al-Mn and Al-Fe-Mn systems carried out at Alean International during the course of the project, have proven essential to our understanding of the experimental uncertainties and to the development of the database. 2 Data Assessment 2.1 Al-Mn system The calculated phase diagram for this system is shown in Fig 1. The phase diagram data for this binary system, crucial to the present project, has caused great concern due to experimental inadequacies. Much painstaking work and careful analyses of the available information has been carried out both in the present work and by others in the field. The experimental data, particularly for equilibria involving Al 4 Mn, are fraught with problems due to the appearance of metastable phases, rather than the stable phase, see eg, [87Mur/McA, 87 McA/Mur, 92Jan, 96Wei/Rog]. This leads to low, nonequilibrium liquidus temperatures, which, however, are consistently reproduced by different experimental studies. For the present project the most important part of the system is the range 0 to 4 or 6 wt % Mn, although for multicomponent calculations it is important to have a good overall representation of the system. For the Al-rich region the prime data source is due to Phillips [43Phi], coupled with recent data from University of Manchester/UMIST [95Hay/Rob], now more generally available [96Wei/Rog], carried out using a sophisticated calorimetrie technique, and data of Thornton [96Tho4]. In addition Sigli [95Sig] has redetermined the solid solubilities of Mn in fcc Al. The current analysis takes into account a revision of the original [43Phi] thermal analysis data by Phillips himself, reported obscurely in an evaluation of the Al-Mn-Si system [59Phi] (see also [61Phi]), and includes information obtained on heating, rather than cooling, by [33Dix/Fin, 87McA/Mur], which avoids the problem of undercooling. The data of [96Wei/Rog] and [96Tho4] have been incorporated. Figs 2-4 show calculated phase equilibria for the Al-rich part of the system. Fig 2 shows the undercooling effects observed over the composition range 10 - 30 wt % Mn, almost - 258 -
certainly due to the appearance of metastable phases, and Fig 3 shows the corrected [59Phi] information together with a single value of [33Dix/Fin] at = 10 % Mn, and the recent data of [96Tho4]. The fcc solvus is shown in Fig 4. The current re-assessment, which is a modified and improved version of that in the COST 507 database [92Jan], represents a very satisfactory outcome. 2.2 Al-Fe-Mn System During the course of the current project new experimental information concerning the solid-state equilibria has been determined by Thornton [95Thol, 95Tho2] at 570 and 600 °C, and liquidus data have been determined at University of Manchester/ UMIST [95Hay/Ser] to corroborate the 2 wt % Mn isopleth due to [43Phi]. In addition solidstate equilibria at 550 °C by Rogl, Universität Wien [95Wei/Rog], [95Rog], have been made available to the project. These latter data are now more generally available [96Wei/Rog]. An optimisation has been carried out whereby substantial consistency between the lowtemperature (570 and 600 °C) solid-state data of [95Thol, 95Tho2], the solid-state data of Rogl (550 °C) [96Wei/Rog], and the liquidus data of Phillips [43Phi] (allowing for expected undercooling, see Section 2.1), and Hayes [95Hay/Ser], has been achieved. The revised data for the Al-Mn system have been incorporated. Figs 5 and 6 show calculated partial isothermal sections for 873 and 843 K, with the results of [95Thol, 95Tho2] superimposed. Fig 7 shows a calculated partial isothermal section for 823 K, with the results of [96Wei/Rog] superimposed. Fig 8 shows the calculated isopleth for a constant 2 wt % Mn. Experimental data of [43Phi], [95Hay/Ser] and [96Thol, 96Tho2, 96Tho3] are superimposed. Figs 9 and 10 show the calculated fcc solvus at 823 and 873 K respectively, with experimental data made available by SINTEF [95Sim/Kol] and due to Hamerton [96Ham] superimposed. Figs 5-10 show that substantial agreement between the experimental data and the current assessment has been achieved. Fig 8 indicates the undercooling experienced by [43Phi] (these experimental values were not corrected by Phillips), and probably reflects the true situation. It has not yet been possible to obtain agreement with all of the data due to Thornton without unreasonable stabilisation of the Al 6 (Mn,Fe) phase and an accompanying unreasonable raising of the liquidus curve. The data for 3, 3.25 and 3.5 wt % Fe are currently under review by Thornton; with respect to Fig 8 it may be that very small amounts of Al ]3 (Fe,Mn) 4 were present, but extremely difficult to detect. 3 Conclusions and Recommendations for Further Work The current thermodynamic data assessments for the binary system Al-Mn and the ternary system Al-Fe-Mn represents a significant milestone for the overall project, and a considerable advancement in our knowledge of phase diagram information for these two systems. Subject to further limited confirmatory experimental studies, the assessment of data for these two systems can now be regarded as substantially complete. Completion of the above paves the way for completion of data for the Al-Mn-Si system, both experimental studies (in progress at Alean International Ltd, Banbury - 259 -
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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°
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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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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
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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: A Thermochemical Assessment of Data
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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