COST 507 - Repositório Aberto da Universidade do Porto

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Experimental Investigations in Ternary and Quaternary Ti-Al- Metal Systems D8 Erich Lugscheider, Klemens Schlimbach, Lehr- und Forschungsgebiet Werkstofrwissenschaften, RWTH Aachen, Germany Manfred Koschlig, Degussa AG, Hanau, Germany and Ingo Reinkensmeier, Eurobras GmbH, Menden, Germany Abstract This research forms part of the COST 507-Π programme on the Ti-Al-Me-Me system (Key System 5). Within these work alloys of the system Ti-Al-Cu-Ni are investigated concerning its density, oxidation behaviour (825°C/15h), phase transition- and melting temperature for both conditions the molten and annealed state. Furthermore wetting - and joining tests were carried out on Ti 3 Al- and TiAl-base material with alloys which have a good oxidation behaviour and a suitable melting temperature. 1 Introduction The intermetallic a 2 -Ti 3 Al and γ-TiAI alloys possess particular mechanical and physical properties which make them of interest for use as structural materials in the aerospace and aircraft industries. In contrast to conventional Ti based alloys, the Titaniumaluminides have a higher resistance to oxidation and exhibit significantly less sensitivity to hydrogen embrittlement. These materials are able to exceed the application temperature of advanced Ti-alloys and also have the potential to replace nickel-based superalloys up to 800°C. Brazing seems to be the most successful joining method for this materials because of its less process temperature. Hence, the influence of the base material by a brazing process is much smaller than by a welding process. For the development of new filler metals for TLAl-based materials the knowledge of the metallurgical reactions between the filler metal and the base material is an important aspect; a further feature is a detailed investigation of the filler metals themselves. This includes the determination of the phases with X-ray diffraction, thermal analysis (ascertain the phase transition temperatures and melting ranges), determination of density and metallografie investigations (light- and electronmicroscopy). - 90 -
Material and Methods 2.1 Fabrication of the alloys The components of the alloys are weigh in with a precision of 0,01 g (corresponding to =0,1 wt.-%). The elements are molten in an arc-beam furnace by using a thoriated tungsten cathode and a water cooled copper crucible (anode). All alloys were molten four times in an argon atmosphere to guarantee a homogeneous distribution of the elements. As for the various investigations afterwards only, small parts of the fabricated alloys are necessary the samples are crushed mechanically. Fig 1 gives an overview about the composition of the investigated alloys. weigjrt- Investigated alloys in the system Ti-Al-Ni-Cu % ha Fig. 1: Composition of the investigated alloys 2.2 Base material The base material used for wetting- and joining tests is Ti48A12Cr2Nb [at-%]. This material was produced by Plansee AG, Reutte, (Au), which has developed a special rolling process to produce sheets. The microstructure of this γ-TiAl material has the formation of a so-called „near gamma" microstructure. This microstructure consists of equiaxial γ-TiAl grains and small amounts of a 2 -Ti 3 Al at triple points and grain boundaries. The following table shows the characteristic temperatures. Til5AlNb Ti48A12Cr2Nb Tuq. 1050°C 1500°C TBraze 900°C 1250°C Fig. 2: Melting and brazing temperatures of the used base materials 91 -
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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
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: 84Bey R. Beyers, R. Sinclair, and M
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
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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) —
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An Experimental Investigation of th
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An Experimental Investigation of th
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EXPERIMENTAL INVESTIGATION OF THE C
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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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