COST 507 - Repositório Aberto da Universidade do Porto

More documents

Recommendations

Info

A Thermochemical Assessment of Data for the Al-rich Corner of the of the Al-Mn-Si System Abstract Malcolm H Rand," Per Kolby* and Tim G Chart* 'WintersHill Consultancy, Abingdon, Oxfordshire, UK *SINTEF, Oslo, Norway *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 provides an optimisation of data for the Al-rich corner of the Al-Mn-Si ternary system, which in addition to the available published data, incorporates the results of experimental measurements carried out during the Action by Alean International Ltd (Banbury Laboratory), Pechiney Centre de Recherches de Vorrepe, SINTEF and University of Manchester/UMIST, and incorporates a revision of data for the binary Al-Mn system, based upon the original COST 507 assessment for this system [92Jan, 94Ans]. The results of the assessment 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 information is required, particularly to define unambiguously the relative stabilities of the cubic alpha, hexagonal beta and liquid phases. The solid phases are not easy to nucleate, and the associated thermal effects are small, so quite detailed and careful experimentation is required to produce reliable results. 246 -
1 Introduction and Overview of the System The Al-Mn-Si system is of crucial importance in the evaluation of the Al-Fe-Mg-Mn-Si quinary system, since one of the important phases in commercial alloys, eg for canning and recycling, is based on the ternary cubic alpha phase in this system. The most recent assessment of the Al-Mn-Si system is by Prince [93Pri]. This necessarily relied heavily on the pioneering work by Phillips [43Phi], (revised slightly in the later publications [59Phi, 61 Phi]), since this is still the only substantial study of the Al-rich corner of the system. Although the overall picture of the Al-Mn-Si system from this work is undoubtedly correct, particularly at low Mn levels, some doubt was thrown on some of Phillips' transition temperatures by the work of Chadwick et al in COST 507 Round I. It is clear that the difference in stability of the phases in many Al- Mn binary and higher systems is quite small, so that effects such as difficulties of nucleation and the presence of small amounts of impurities, eg Fe, can have noticeable effects on the experimental phase diagrams for this system. These effects appear to be particularly relevant to Phillips' study, bearing in mind the likely levels of impurities in Al alloys of the 1940s, and the techniques employed. Recent experimental work on this system initiated as a result of the current project, particulary on the section containing 4 wt% Si, by a combination of Alean International Ltd (Banbury Laboratory) and University of Manchester/UMIST, have confirmed that some of the liquidus temperatures measured by Phillips are indeed substantially (at least 20 K) too low. In addition, new solvus data which differ appreciably from those of Phillips have been produced by SINTEF and Pechiney as part of the project [94Kol/Sig]. These data have been incorporated into a new thermodynamic description of this system. This new description reproduces well the data for the 4 wt% Si section, but raises doubts as to the accuracy of the previously available experimental information available in many parts of the system. The phases in this ternary system which are in equilibrium with aluminium are Al 6 Mn, Al 4 Mn and two ternary phases, usually called alpha and beta. These are different in both composition and structure from the similarly-named phases in the Al-Fe-Si system. 2 Phase diagram As noted above, the only systematic study of the system was carried out by Phillips more than fifty years ago, with some more recent work at silicon levels close to the binary ΑΙ-Si eutectic (c. 12 wt% Si) [88Zak/Gul] and data for equilibria between liquid, beta and cubic-alpha at 1027 K by Redford et al [90Red/Tib]. Axon and Hume- Rothery [48Axo/Hum] also gave partial sections at 460 °C, but they may not correspond to true equilibrium. The liquidus projection suggested by Prince [93Pri] is very similar to that proposed by Phillips [59Phi, 61 Phi] in his revision of his earlier work. However, thermal analysis work during COST 507 Round I suggested that some of the liquidus temperatures on this diagram were appreciably too low - particularly those for the separation of the complex cubic-alpha and beta phases. - 247
Page 1 and 2:
European Commission COST European c
Page 5 and 6:
European Commission COST European c
Page 7:
Preface The Final Workshop of the C
Page 11 and 12:
COST 507 STRUCTURE Measurement and
Page 13:
GRl: Mirtee S.A., Volos Mr.P.Polati
Page 16 and 17:
D9 Dll Fl GR2 II NI S3 SF1 "Thermop
Page 19 and 20:
A Summary of the COST 507 Action an
Page 21 and 22:
Aluminium-based systems Titanium-ba
Page 23 and 24:
An Example using the COST 507 Datab
Page 25 and 26:
Appendix COST 507: Some Key Meeting
Page 27 and 28:
Al - 0.5 Fe, 1 Mg, 0.8 Mn, 0.2 Si (
Page 29 and 30:
Fig 4 Aluminium beverage cans. The
Page 31:
Fig 6 High pressure compressor vane
Page 34 and 35:
INTRODUCTION All of us are aware of
Page 36 and 37:
In the interaction with materials a
Page 38 and 39:
There was a first warning more than
Page 40 and 41:
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 and 92:
satisfied the three requirements of
Page 93 and 94:
84Bey R. Beyers, R. Sinclair, and M
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
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 and 170:
eviews by Rivlin and Raynor [81 Riv
Page 171 and 172:
inaires. Thesis, Universite Scienti
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
Page 215 and 216: 211 -
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: 0.2 0.3 0.4 0.5 X(LIQ,V) Figure 15
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
Page 279: European Commission EUR 18171 —CO
Page 284: NOTICE TO THE READER Information on
show all

COST 507 - Repositório Aberto da Universidade do Porto

Create successful ePaper yourself

Delete template?

Save as template?