Journal of Materials Science

, Volume 47, Issue 24, pp 8381–8386 | Cite as

Sessile drop study of Gd–Ti monotectic alloys on ceramic substrates: phase transformations, wetting, and reactivity

  • I. Kaban
  • R. Nowak
  • O. Shuleshova
  • B. Korpala
  • G. Bruzda
  • A. Siewiorek
  • J. H. Han
  • N. Sobczak
  • N. Mattern
  • J. Eckert
Open Access
HTC 2012

Abstract

Gd–Ti monotectic alloys were studied in a wide temperature range by the sessile drop technique. The eutectic and monotectic transformations in Gd–Ti alloys upon heating were in situ monitored by a high-speed and high-resolution CCD camera. Our findings suggest that the existing Gd–Ti phase diagram significantly underestimates the monotectic and binodal temperatures in this system. The wetting behavior and the high-temperature interaction of the Gd–Ti melts with yttria and yttria-stabilized zirconia substrates were investigated.

Keywords

Y2O3 Sessile Drop Sessile Drop Technique Monotectic Temperature Monotectic Alloy 

Introduction

According to the equilibrium phase diagram [1], the Gd–Ti system exhibits a miscibility gap in the liquid state. This makes Gd–Ti-based multicomponent alloys appropriate for fabrication of nano- and microphase-separated composite materials. Such composites have a high application potential due to combination of two or more phases with remarkably different properties. The microstructure of solid alloys that exhibit a liquid–liquid miscibility gap is determined by their thermophysical properties and casting conditions (see, for example, refs. [2, 3, 4, 5, 6, 7, 8] and citations therein). The Gd–Ti system also plays an important role in the synthesis of high-performance alloys for magnetic applications by alloying, for example, with Ge, Mn, Fe, and Sn [9, 10, 11, 12]. These materials are usually produced by melting of pure components and subsequent homogenization of the melts at certain temperatures determined from the respective phase diagrams. Therefore, knowledge of thermodynamic and thermophysical properties of the molten alloys is of high practical importance. In this context, accurate data on the binary systems are indispensable.

In this work, we investigated binary Gd–Ti alloys upon heating by the sessile drop technique. Due to the use of a high-speed and high-resolution charge-coupled device (CCD) camera, it was possible to record the wetting behavior and the high-temperature interaction of the Gd–Ti melts with yttria and yttria-stabilized zirconia substrates. Moreover, this technique allowed real-time observation of the eutectic and monotectic phase transformations in the Gd–Ti alloys. The microstructure of solidified Gd–Ti bulk samples as well as the interfaces formed in the sessile drop investigations between Gd–Ti alloys and ceramics were characterized by scanning electron microscopy (SEM) combined with energy-dispersive X-ray (EDX) spectrometry.

Experimental procedures

Gd40Ti60 and Gd60Ti40 alloys were selected for the investigations. According to the Gd–Ti phase diagram [1], both alloys fall into the liquid miscibility gap: Gd40Ti60—close to the monotectic composition x M = 35 at.% Gd and Gd60Ti40—close to the critical composition x C ≈ 63 at.% Gd (Fig. 1). Samples of nearly spherical shape with about 800 mg mass were prepared by arc-melting of high purity elements (99.99 % or higher) under an argon atmosphere.
Fig. 1

Gd–Ti phase diagram [1]. Vertical dashed lines point to the compositions studied in this work; circles mark the maximum temperature achieved in the sessile drop experiments

Polycrystalline yttria (Y2O3) and two kinds of yttria-stabilized zirconia (ZrO2 stabilized with 3 wt.% of Y2O3 ≡ 3YSZ and ZrO2 stabilized with 5 wt.% of Y2O3 ≡ 5YSZ) were used as substrates in the sessile drop experiments. The substrates were polished with the same oxide powder that was used for the sintering of the ceramics, to avoid their pollution.

The sessile drop investigations were carried out using the experimental setup described in details in ref. [13]. Before loading into the UHV chamber equipped with a vertical resistance heater, the Gd–Ti samples and substrates were cleaned ultrasonically in isopropanol for 5 min. Heating was started when the level of vacuum reached at least 10−6 mbar. At 500 °C, high purity Ar (99.999 %) was introduced into the chamber. The flow rate was 5 cm3 min−1 and the pressure level inside the high-temperature chamber was held in the range of 850–900 mbar. The heating rate was 6 K min−1 and the cooling rate was 18 K min−1.

The behavior of the Gd–Ti samples on ceramic substrates was registered by a high-speed and high-resolution CCD camera. The experiments were performed from room temperature up to some degrees Kelvin above the point, where Gd–Ti droplets looked as being completely melted. At the first stage of heating up to 1000 °C, the drop image acquisition was 1 fps (frame per sec), after that it was increased to 100 fps.

After cooling, the Gd–Ti/substrate couples from the sessile drop experiments were cut in the central part perpendicular to the substrate surface and their microstructure and composition characterization was performed with Hitachi TM3000 SEM microscope equipped with an EDX analyzer.

Results

The first sessile drop tests with the Gd40Ti60 and Gd60Ti40 alloys were carried out using Y2O3 substrates. Incipient melting for both compositions was observed at about 1240–1250 °C, when the Gd-rich liquid filled the gap between the sample and the substrate. The volume fraction of the liquid phase increased upon further heating. However, the alloys were not completely molten at 1275 °C, as predicted by the calculated phase diagram [1] (Fig. 1). A skeleton of the lighter Ti-rich solid phase was observed to “float” on the Gd-rich liquid. At ~1350 °C, the liquid phase began to wet the yttria substrate and at ~1430 °C began to penetrate it. The heating was stopped at 1450–1460 °C, when almost the whole substrate was penetrated by the Gd-rich liquid. For illustration of the described phenomenon, three images for the Gd60Ti40 composition taken during heating at 1370, 1410, and 1450 °C, and an image of the Gd60Ti40/Y2O3 couple after the experiment are shown in Fig. 2. The same behavior has been observed for the Gd40Ti60 composition.
Fig. 2

ac Images of the Gd60Ti40 alloy on Y2O3 substrate taken during heating in a sessile drop experiment; d image of the Gd60Ti40/Y2O3 couple after the high-temperature test. Gd-rich liquid wets the Ti-rich solid phase as well as the substrate. At 1450 °C, all available Gd-rich liquid penetrates the substrate

Due to infiltration of molten Gd-rich phase into Y2O3 as described above, ZrO2 stabilized with Y2O3 was chosen as an alternative substrate material. Still notable reaction between the Gd–Ti melts and ceramic was observed in the case of 5YSZ (not shown), while the substrates made of 3YSZ were quite stable and resistant against molten Gd–Ti. Selected sessile drop images of the Gd40Ti60 and Gd60Ti40 alloys on the 3YSZ ceramics are shown in Figs. 3 and 4, respectively. Similar to the studies carried out on the Y2O3 substrates, melting of these compositions starts at about 1220–1230 °C (Figs. 3a, 4a). At ~1370 °C, the Gd-rich phase begins to wet 3YSZ substrate, but it does not penetrate the substrate. After the incipient melting, the shape of both Gd40Ti60 and Gd60Ti40 samples remains quite irregular over a wide temperature range: the bottom part of the semi-solid drop—heavier Gd-rich liquid phase—is rather symmetrical, while the upper part is asymmetrical due to the floating solid Ti-rich phase. The drops become axisymmetrical at ~1620 °C for Gd60Ti40 and at ~1654 °C for Gd40Ti60 indicating that the samples are completely molten.
Fig. 3

Images of the Gd40Ti60 alloy on a 3YSZ substrate taken at various temperatures. At about 1230 °C, the sample starts melting; it is completely molten at 1654 °C

Fig. 4

Images of the Gd60Ti40 alloy on a 3YSZ substrate taken at various temperatures. The sample starts melting at about 1220 °C; it is completely molten at about 1620 °C

Initially white, ZrO2 stabilized with 3 wt.% Y2O3 became light gray in the region surrounding Gd–Ti drop after the high-temperature tests (Fig. 5); but unlike other substrates used in this study, there was no obvious penetration of the liquid phase into the 3YSZ (Fig. 6a, b). Instead, GdZrO crystals (up to about 10 μm in length) were observed on the ceramic surface outside the Gd–Ti drop, as demonstrated in Fig. 6c.
Fig. 5

Gd40Ti60 (a) and Gd60Ti40 (b) alloys on 3YSZ substrates after sessile drop investigations

Fig. 6

SEM images of the cross section for the Gd-Ti samples on the 3YSZ substrates after sessile drop investigations: a Gd40Ti60, b Gd60Ti40, c image taken at the outer edge of the Gd40Ti60 drop as marked by a rectangle in the panel b: GdZrO crystals have grown on the substrate outside the sample/substrate contact zone, and d image taken at the top of the Gd60Ti40 sample: Ti–rich phase (dark) is covered by a thin layer of the Gd-rich phase (light)

Discussion

It is a challenge to find a suitable crucible or substrate material for high-temperature investigations of liquid alloys containing such highly reactive components as Ti and Gd. Y2O3 was reported to be relatively stable against molten Ti [14]; although small quantities of Y and O could be dissolved from the ceramic [14, 15]. On the other hand, liquid Ti and Ti-based alloys severely react with Al2O3 and ZrO2 ceramics [16, 17]. Despite a lack of information on the interaction between liquid Gd and ceramics, a high chemical aggressivity of rare metals is known. Based on the literature data on reactivity of Ti-based alloys, the polycrystalline Y2O3 substrates were selected for our first sessile drop tests. However, they were quickly penetrated by the liquid Gd phase, as demonstrated in Fig. 2. This well-distinguished infiltration of the first liquid into Y2O3 enabled a visual observation of the two-phase state (Ti-rich solid and Gd-rich liquid) in the Gd–Ti system at the temperatures between 1240 and 1460 °C.

It should be noted that just a very small quantity of Y (0.1–0.3 at.%) was found in the Ti-rich phase solidified on the yttria substrate. We suppose that Y could have appeared there either due to a slight dissolution of the substrate during the sessile drop tests or during the cutting and subsequent polishing of the Gd–Ti/Y2O3 couples for the SEM/EDX characterization, or both.

The situation has been essentially changed in the case of yttria-stabilized zirconia. Neither Ti nor Gd was found in the drop-side region of the 3YSZ substrates after the sessile drop tests. Pollution of the Gd–Ti sample due to interaction with the ZrO2 substrate was very small (about 0.5–1 at.% Zr in some solidified drops was detected by EDX). It has been reported in ref. [18] that the high-temperature (1400 °C) solid-state reaction and interdiffusion between yttria-stabilized zirconia and GdCeO is suppressed due to the formation of a thin (≤1 μm) interaction zone. A similar phenomenon might occur at the contact of Gd-rich liquid and YSZ ceramic. It is plausible that a thin GdZrO layer is formed at the interface and prevents interdiffusion of components and further growth of the reaction zone. At the same time, Gd atoms may diffuse from the Gd liquid phase along the ceramic surface feeding the growth of GdZrO crystals in the vicinity of the drop, as observed in Fig. 6c. Obviously, GdZrO grows on the expense of Zr and O from the 3YSZ substrate. The loss of oxygen resulting in the formation of a nonstoichiometric ZrO2−x [19] could explain gray coloring of the substrates, noted during the high-temperature tests.

The melting temperature for the Gd-rich phase in the Gd40Ti60 and Gd60Ti40 alloys (1220–1250 °C) determined upon heating in the present sessile drop studies on all substrates shows a good agreement with the eutectic isotherm (T E = 1240 °C) from the Gd–Ti phase diagram [1]. However, the tests carried out on the Y2O3 substrates revealed that the monotectic temperature (T M = 1275 °C) in the phase diagram (Fig. 1) is significantly underestimated. Indeed, the Ti-rich phase remained solid until 1450–1460 °C in those experiments. As it has been established in the sessile drop measurements performed on the 3YSZ ceramics, the Ti-rich phase melts at about 1620–1650 °C. Comparison of the images of the Gd40Ti60 and Gd60Ti40 sessile drops (Figs. 3e, 4d, e) with the experimental and calculated sessile drop profiles for the Ga–Pb phase-separated melts studied close to the respective monotectic temperature in ref. [20] suggests that the Gd–Ti alloys at 1620–1650 °C are rather in a two-phase liquid state than a single-phase liquid. The Gd40Ti60 and Gd60Ti40 samples after the sessile drop investigations on the 3YSZ substrates exhibit macroscopic phase separation (Fig. 6a, b). The oval-like shape of the Ti-rich phase, distorted during crystallization, and its location inside the Gd-rich phase at the top of the samples also indicates that the alloys were completely molten and both fall into the miscibility gap.

The melting temperature for the Ti-rich phase following from our study is about 350–400 K above the calculated monotectic temperature [1] and about 190–240 K above the melting temperature reported in ref. [21]. Such a big difference cannot be an effect of the applied heating rate, which is rather moderate (6 K min−1), since the liquid phase is already present (recall that the Gd-rich phase melts at 1240 °C). Also, the melting temperature of the Ti-rich phase is unlikely to be influenced by a very small quantity of either Y or Zr found mainly in the Gd-rich phase after the high-temperature tests. The large disagreement of the experimental results can be explained by the different techniques applied in the present work (sessile drop method) and in ref. [21] (thermal-gradient method [22]). The thermal-gradient method, in which melting is detected by optical observation of a cavity in the sample, is rather uncertain in two-phase melting alloys, as the cavity is usually filled by the first liquid or the specimen collapses before the second phase completely melts [23]. It should also be noted that the melting data reported in ref. [21] suffered large scattering and were severely reinterpreted during calculations [1]. Our findings suggest that the liquid state equilibria in the Gd–Ti phase diagram [1] should be reassessed.

The Ti-rich phase in the Gd–Ti samples solidified after the sessile drop measurements was completely covered by about 5–40 μm thick layer of the Gd-rich phase as it can be seen on the SEM/EDX image in Fig. 6d. Earlier, such surface wetting layers have been observed in other monotectic alloys; for example in Ga–Bi [24], Ga–Pb [25], Cu–Co [26], and Al–In [27]. Calculations showed that complete wetting is preserved in many immiscible systems far below the monotectic or even eutectic temperature [27, 28, 29], and this has been related to the high surface tension σ of metallic liquids. Bearing in mind that σ of the liquid Gd is ~800 mN m−1 at 1600 °C [30] and σ of the liquid Ti is ~1450 mN m−1 at 1700 °C [31], it is reasonable to suppose that the Gd-rich phase completely wets the Ti-rich phase in the liquid Gd–Ti alloys and the equilibrium wetting layer grows by diffusion up to a micrometer thickness during solidification as it has been suggested in ref. [27].

Summary

The sessile drop technique equipped with a high-speed and high-resolution CCD camera was used for in situ observation of the eutectic and monotectic phase transformations in the Gd–Ti alloys as well as of the high-temperature interaction of the melts with yttria and yttria-stabilized zirconia substrates.

The observed eutectic transformation in the Gd40Ti60 and Gd60Ti40 alloys at about 1220–1250 °C is in a good agreement with the experimental [21] and calculated [1] Gd–Ti phase diagram. In contrast, the monotectic temperature determined by the analysis of the Gd–Ti sessile drop images taken by a high-speed/high-resolution CCD camera lies between 1620 and 1650 °C, which significantly exceeds the monotectic temperature (1275 °C) calculated in ref. [1]. After the high-temperature tests, the surface of the Ti-rich phase in the solidified Gd–Ti samples is covered by a micrometer-thick layer of the Gd-rich phase suggesting that complete wetting in the Gd–Ti system occurs in a wide temperature range above and below the monotectic temperature.

The Gd-rich liquid phase of the semi-solid Gd40Ti60 and Gd60Ti40 alloys wets Y2O3 at about 1350 °C and penetrates the ceramic at 1430–1450 °C. The Gd–Ti melt reacts relatively strongly with the ZrO2 substrates containing 5 wt.% Y2O3. The substrates made of the ZrO2 stabilized with 3 wt.% Y2O3 are stable at contact with the Gd–Ti melts over a wide temperature range up to about 1650 °C.

Notes

Acknowledgements

This study has been carried out in the frame of the German–Polish collaboration program between the German Academic Exchange Service DAAD (Project No. DAAD50755060) and the Ministry of Science and Higher Education of Poland (Project #002/2011/2012). DAAD and the Foundry Research Institute in Cracow are acknowledged for the financial support.

Open Access

This article is distributed under the terms of the Creative Commons Attribution License which permits any use, distribution, and reproduction in any medium, provided the original author(s) and the source are credited.

References

  1. 1.
    Massalski TB, Murray JL, Bennet KH, Baker H (1990) Binary alloy phase diagrams, 2nd edn. American Society for Metals, Metals Park, p 1935Google Scholar
  2. 2.
    Chattopadhyay K, Ramachandrarao P (1980) J Mater Sci 15:685. doi: 10.1007/BF00551735 CrossRefGoogle Scholar
  3. 3.
    Prinz B, Romero A, Ratke L (1995) J Mater Sci 30:4715. doi: 10.1007/BF01153083 CrossRefGoogle Scholar
  4. 4.
    Fujii H, Kimura T, Kitaguchi H, Kumakura H, Togano K, Mohri M (1995) J Mater Sci 30:3429. doi: 10.1007/BF00349890 CrossRefGoogle Scholar
  5. 5.
    Yang S, Liu W, Jia J (2001) J Mater Sci 36:5351. doi: 10.1023/A:1012467817033 CrossRefGoogle Scholar
  6. 6.
    Rathz TJ, Robinson MB, Li D, Workman GL, Williams G (2001) J Mater Sci 36:1183. doi: 10.1023/A:1004885926618 CrossRefGoogle Scholar
  7. 7.
    Zhao J, Ratke L, Jia J, Li Q (2002) J Mater Sci Technol 18:197Google Scholar
  8. 8.
    Kaban I, Köhler M, Ratke L, Nowak R, Sobczak N, Mattern N, Eckert J, Greer AL, Sohn SW, Kim DH (2012) J Mater Sci. doi: 10.1007/s10853-012-6660-3
  9. 9.
    Morozkin AV (1999) J Alloy Compd 287:185CrossRefGoogle Scholar
  10. 10.
    Jingqi L, Jiqin Q, Ren D, Yinghong Z, Jinli H (2006) J Alloy Compd 414:97CrossRefGoogle Scholar
  11. 11.
    Ma J, Zhan Y, Zhang G, Guo Q, Du Y, He Y (2009) J Alloy Compd 485:196CrossRefGoogle Scholar
  12. 12.
    Ma J, Zhan Y, She J, Yang Z, Liang J (2010) J Alloy Compd 489:384CrossRefGoogle Scholar
  13. 13.
    Sobczak N, Nowak R, Radziwill W, Budzioch J, Glenz A (2008) Mater Sci Eng A 495:43CrossRefGoogle Scholar
  14. 14.
    Helferich RL, Zanis CA (1973) Naval Ship Research and Development Center, Rep. 28-409, Annapolis, MDGoogle Scholar
  15. 15.
    Naidich YV (1981) Progress in surface and membrane science, vol 14. Academic Press, New York, p 353Google Scholar
  16. 16.
    Nowak R, Lanata T, Sobczak N, Ricci E, Giuranno D, Novakovic R, Holland-Moritz D, Egry I (2010) J Mater Sci 45:1993. doi: 10.1007/s10853-009-4061-z CrossRefGoogle Scholar
  17. 17.
    Lin KF, Lin CC (1998) Scr Mater 39:1333CrossRefGoogle Scholar
  18. 18.
    Tsoga A, Gupta A, Naoumidis A, Nikolopoulos P (2000) Acta Mater 48:4709CrossRefGoogle Scholar
  19. 19.
    Gladkov VE, Berezin VM, Zhekhanova NB (2010) Inorg Mater 46:754CrossRefGoogle Scholar
  20. 20.
    Chatain D, Wynblatt P, de Ruijter M, de Conninck J, Carter C (1999) Acta Mater 47:3049CrossRefGoogle Scholar
  21. 21.
    Croeni JG, Rhoads SC, Armantrout CE, Kato H (1961) U.S. Bureau of Mines, Rep. Invest. 5796, Washington, DCGoogle Scholar
  22. 22.
    Pirani M, Alterthum H (1923) Z Elektrochem 29:5Google Scholar
  23. 23.
    Rudy E, Progulski J (1967) Planseeber Pulvermetall 15:13Google Scholar
  24. 24.
    Perepezko JH, Galaup C, Cooper KP (1982) Mater Res Soc Symp Proc 9:491CrossRefGoogle Scholar
  25. 25.
    Calmes C, Giuranno D, Chatain D (2009) J Mater Sci 44:5949. doi: 10.1007/s10853-009-3563-z CrossRefGoogle Scholar
  26. 26.
    Curiotto S, Battezzati L, Johnson E, Pryds N (2007) Acta Mater 55:642CrossRefGoogle Scholar
  27. 27.
    Kaban I, Curiotto S, Chatain D, Hoyer W (2010) Acta Mater 58:3406CrossRefGoogle Scholar
  28. 28.
    Chatain D, Eustathopoulos N, Desre P (1984) J Colloid Interface Sci 83:384CrossRefGoogle Scholar
  29. 29.
    Wynblatt P, Saul A, Chatain D (1998) Acta Mater 46:2337Google Scholar
  30. 30.
    Ichikawa T, Okada JT, Paradis PF, Watanabe Y (2010) Int J Thermophys 31:288Google Scholar
  31. 31.
    Zhu J, Kamiya A, Yamada T, Shi W, Naganuma K, Mukai K (2002) Mater Sci Eng A 327:117CrossRefGoogle Scholar

Copyright information

© The Author(s) 2012

Authors and Affiliations

  • I. Kaban
    • 1
  • R. Nowak
    • 2
  • O. Shuleshova
    • 1
  • B. Korpala
    • 2
  • G. Bruzda
    • 2
  • A. Siewiorek
    • 2
  • J. H. Han
    • 1
  • N. Sobczak
    • 2
  • N. Mattern
    • 1
  • J. Eckert
    • 1
    • 3
  1. 1.Institute for Complex MaterialsIFW DresdenDresdenGermany
  2. 2.Center for High Temperature StudiesFoundry Research InstituteKrakówPoland
  3. 3.Institute of Materials ScienceTU DresdenDresdenGermany

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