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Platinum Metals Rev., 1967, 11, (4), 132

The Platinum-Molybdenum System

The Formation of Intermediate Phases

  • By G. L. Selman, B.Sc.
  • Research Laboratories, Johnson Matthey & Co Limited
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Article Synopsis

Although platinum-clad molybdenum is used extensively as a material for handling molten glass, surprisingly little is known about the constitutional relationships in this refractory metal binary system. Recent work in the Johnson Matthey Research Laboratories has confirmed that the published equilibrium diagram is incomplete and that four intermediate phases are formed at high temperatures. This work has provided a better understanding of the behaviour of platinum-clad molybdenum equipment under operating conditions in the glass industry.

Advances in glass technology, leading in many instances to increased handling temperatures, are placing an ever-increasing burden upon glass handling equipment. Emphasis is being placed more and more on the use of composite materials, such as molybdenum with an outer cladding of platinum, which take advantage of both the excellent high temperature mechanical properties of the refractory metals and the outstanding oxidation resistance and general chemical inertness of the platinum metals.

While the stirrers, mandrels and electrodes constructed of platinum-clad molybdenum have useful lives at temperatures of up to 1200°C, at higher temperatures, although this combination represents the most economic and technically satisfactory choice, inter-reaction between the two metals takes place, so that the life of the platinum sheath is largely dictated by the rate at which molybdenum diffuses through it and by the effect of the intermediate alloy layers so formed upon its integrity.

It is therefore becoming increasingly important to the metallurgist concerned with this problem that he has at his command sound information concerning the binary alloys of the platinum metals with the refractory metals at temperatures up to 1500°C. Such information is not generally available in the literature.

During the course of recent diffusion studies made in these laboratories on molybdenum rods mechanically clad with platinum sheaths, metallographic evidence confirming the existence of four intermediate alloy phases in this complex binary system has been obtained. The solubility of platinum in molybdenum in the temperature range 1400°C to 1700°C has also been determined by direct analysis of the microstructure of two molybdenum-rich alloys made by conventional alloying techniques. The solubility has been found to increase rapidly with temperature in this region. The results of this investigation bear interesting comparison with the previous studies made on this system.

Previous Constitutional Work


The earliest reference to the platinum-molybdenum system appears to be that due to Dreibholz (1) who suggested that about 16 weight per cent molybdenum should be soluble in platinum at the eutectic temperature, this figure decreasing to less than two per cent at room temperature. Hultgren and Jaffee (2) studied electron beam melted alloys containing up to 50 atomic per cent molybdenum after annealing at 1000°C. The X-ray patterns that were obtained showed a single face centred cubic phase, with lattice constants near to that of platinum, for all compositions.

The first systematic investigation was carried out by Raub (3) who studied arc melted alloys. He observed very little solubility of platinum in molybdenum but found that molybdenum was appreciably soluble in platinum. He detected a tetragonal distortion of the face centred cubic lattice in platinum-rich alloys containing more than about 25 atomic per cent (14 weight per cent) of molybdenum to give an axial ratio greater than 1.0. This new phase, denoted α1, separated from the terminal solid solution below 1400°C. A hexagonal close packed ε phase was found to form at about Pt3Mo2, with a very wide composition range. Further references to this hexagonal phase were made by Greenfield and Beck (4) and Nishimura (5). The latter author constructed an equilibrium diagram on the basis of melting point determinations, X-ray analyses and microscopical examinations. Platinum-rich alloys were shown to form via a peritectic reaction,

and molybdenum rich alloys formed via a eutectic

Nishimura ascribed the composition PtMo to the hexagonal phase, and his diagram suggests an appreciable solubility of platinum in molybdenum at the eutectic temperature.

Nishimura did not account for the tetragonal phase in his work, and the constitutional diagram representing the best combination of evidence available at that time is that due to Knapton (6), reproduced in Fig. 1. It is obvious that no attempt has been made to determine the phase boundary positions accurately, and this diagram can only be regarded as tentative.

Fig. 1

Tentative constitutional diagram of the molybdenum-platinum system as proposed by Knapton (6). The present studies have confirmed that two additional intermediate phases exist, and have also shown that the solubility of platinum in molybdenum is considerably higher than the diagram would suggest at temperatures above 1400°C

Tentative constitutional diagram of the molybdenum-platinum system as proposed by Knapton (6). The present studies have confirmed that two additional intermediate phases exist, and have also shown that the solubility of platinum in molybdenum is considerably higher than the diagram would suggest at temperatures above 1400°C

The first suggestion that the diagram was incomplete came from Kirner (7) who claimed to have observed a new phase, stable only at high temperatures, at the molybdenum-rich end.

Figure 1 illustrates the lack of previous experimental work in this region, and it is not too surprising that such a phase remained undetected. The phase was very hard, and readily observable in both arc melted alloys and diffusion couples heat treated at 1400° and 1500°C. It decomposed on heating for 30 hours at 1200°C.

Rooksby and Lewis (8) conducted the most recent study of this system. During their experiments they heated fine platinum-clad molybdenum wires under controlled conditions which produced the intermediate phases in turn on the coating surface, from which X-ray diffraction patterns were then obtained. The compositions of the phases so formed were not determined directly, but were approximately fixed by analogy with other isostructural compounds from the X-ray diffraction data.

Table 1, which is reproduced in part from Rooksby’s paper, lists the phases identified and some typical heat treatments which were required to produce them at the coating surface.


Table 1

Intermediate Phases in the Platinum-Molybdenum System



Phase Structure Heat Treatment
β (Pt3Mo) (α1 Raub) Tetragonal 1000°C for 24 hr
γ (Pt2Mo) Orthorhombic 1100°C for 24 hr
δ (Pt3Mo2) (ε Raub) H.C.P. 1300°C for 1 hr
ε (PtMo3) Cubic A15 1300°C for 24 hr

Rooksby and Lewis thus identified two phases in addition to those originally proposed by Raub, the orthorhombic γ and the β-tungsten structure designated ε. Both of these phases had very narrow composition ranges, judging from the small variations observed in their lattice spacings. The molybdenum-rich phase due to Kirner is thus in all probability PtMo3, isostructural with the β-tungsten phase previously observed in iridium-molybdenum alloys (9).

Experimental Diffusion Studies at High Temperatures


Platinum-molybdenum diffusion couples have been examined extensively in these laboratories in recent times as part of a general investigation into the uses of platinum at high temperatures. Pressure bonded sheets have been found to be unsuitable for long term annealing above 1300°C, due to a tendency for the components to peel apart, and the test specimens which formed the basis for the major part of this work were manufactured from spectrographically pure Murex molybdenum rod and high temperature grade platinum tubing of 0.060 inch wall thickness, containing typically about 0.0075 per cent total impurity.

Short lengths of the molybdenum rod were vacuum sealed into the close fitting platinum tubes, and the two metals were then bonded by lightly hot swaging the assemblies at 1200°C. The annealing tests were conducted in air at 1400°C. The specimens were freely supported in the hot zone of a mullite tube furnace at this temperature for periods up to 2000 hours, following which they were cooled in air and sectioned for metallographic examination. These composite specimens were difficult to etch chemically because of the vastly differing response of the two metals to the etching solution. The microstructures were revealed most clearly by cathodically etching the polished sections in a stream of low pressure argon.

Microstructure and Constitution of the Diffusion Zones


Diffusion couples prepared in the manner described in the foregoing section maintained their integrity throughout the annealing cycle, and no interfacial failures occurred. Fig. 2 shows the diffusion zone formed in a platinum-clad molybdenum specimen by annealing for 1100 hours at 1400°C. The intimately convoluted nature of the intermediate alloy layers, which makes it difficult to isolate and follow the somewhat erratic formation of the phase adjacent to the molybdenum, was a noteworthy and fairly typical feature of the microstructures observed during the course of this work. Rooksby and Lewis showed from their X-ray data that the structural transitions from one phase to the next occur with the minimum of atomic movement and alteration of lattice spacings, in spite of considerable changes in composition. This close relationship between the phases, which resemble a series of discrete but ordered solid solutions, could well account for their somewhat intimate association within the microstructure.

Fig. 2

A molybdenum-platinum interface after annealing for 1100 hours at 1400°C, showing the four intermediate alloy layers formed during the heat treatment. × 200

A molybdenum-platinum interface after annealing for 1100 hours at 1400°C, showing the four intermediate alloy layers formed during the heat treatment. × 200

On close scrutiny it was possible to resolve four intermediate phases in the diffusion zone, in complete agreement with the findings of Rooksby. These phases are defined more clearly in the microhardness and microprobe traverses made across the diffusion zone, shown in Figs 3 and 4.

Fig. 3

A microhardness scan made across the interface shown in Fig. 1. The hardness levels can be readily identified with the microstructure

A microhardness scan made across the interface shown in Fig. 1. The hardness levels can be readily identified with the microstructure

Fig. 4

Electron probe scans for molybdenum and platinum across the interface shown in Fig. 1. The intermediate alloy layers are well defined and can be accurately related to hardness and microstructure

Electron probe scans for molybdenum and platinum across the interface shown in Fig. 1. The intermediate alloy layers are well defined and can be accurately related to hardness and microstructure

The curve of microhardness across the diffusion zone is remarkably similar in shape to those obtained by Kirner, who studied diffusion couples annealed at 1400° and 1500°C. This worker suggested that the peak at the molybdenum-rich end of the traverse was due to his new phase, and identified the second peak with the hexagonal phase discovered by Raub. Comparison of the microhardness curve with the microprobe scan strongly suggests, however, that the hexagonal δ phase is more closely related to the minimum between the two peaks, and that the second peak occurs within the orthorhombic γ phase discovered by Rooksby.

The microprobe traverse confirms Raub’s finding that the terminal solubility of platinum in molybdenum is small at intermediate temperatures, and highlights the extensive composition range of the hexagonal phase.

In an attempt to establish the compositions of the intermediate alloy layers with some accuracy, point analyses were made at 20 kV on each of the four phases shown in the diffusion zone. The radiations used were PtLα and MoLα. After correction for atomic number and absorption effects the values given in Table II were obtained.


Table II

Electron Probe Microanalyses of the Four Intermediate Phases



Phase Mo Pt
Wt.% At.% Wt.% At.%
I 67.5 81.0 31.5 18.5
II 34.0–45.0 51.1–62.5 54.4–65.0 37.0–47.8
IV 18.5–24 31.6–39 77.0–81.3 62.2–67.6

The analyses are quoted to an estimated accuracy of ± 3 per cent. The composition ranges obtained for phases II and IV at 1400°C agree remarkably well with those shown on the tentative diagram due to Knapton (Fig. 1) for the hexagonal (ε) and tetragonal (α1) intermediate phases.

Taken in order, however, they bear little resemblance to the sequence of structures reported by Rooksby, with the possible exception of phase I. Taken in isolation, the analytical results suggest that the atomic arrangements of the four phases correspond to the compositions PtMo3, PtMo, Pt3Mo2 and Pt2Mo, a sequence which is not well supported by any of the previous investigations.

The Solubility of Platinum in Molybdenum


The form of the molybdenum-rich end of the binary system envisaged by Knapton (Fig. 1) appeared from our own results, and from those of Kirner and Rooksby, to be seriously in error.

Alloys containing 10 and 20 weight per cent platinum were prepared, from starting materials of similar purity to those used for the diffusion studies, in an argon arc furnace. The melted buttons were turned and remelted several times, and finally heat treated for seven hours at 1850°C to ensure homogeneity. Samples from each ingot were then annealed at temperatures ranging from 1100 to 1850°C in an argon atmosphere for long periods, quenched and prepared for metallographic examination.

Figs 5, 6 and 7 show microstructures typical of the 20 per cent alloy quenched from 1850°C, 1700°C and 1250°C. Although some grain boundary precipitation has occurred in the sample quenched from 1850°C it would seem that the alloy was substantially a single phase solid solution at the soaking temperature. Untreated filings taken from this specimen gave a diffraction pattern corresponding to a body centred cubic structure with a lattice parameter a = 3.143Å, a value slightly lower than that of pure molybdenum.

Fig. 5

The substantially single phase microstructure of a 20 per cent platinum-molybdenum alloy quenched after annealing for 7 hours at 1850°C. × 200

The substantially single phase microstructure of a 20 per cent platinum-molybdenum alloy quenched after annealing for 7 hours at 1850°C. × 200

Fig. 6

The 20 per cent platinum-molybdenum alloy quenched after annealing for 7 hours at 1700°C, showing the typical high temperature duplex microstructure. × 200

The 20 per cent platinum-molybdenum alloy quenched after annealing for 7 hours at 1700°C, showing the typical high temperature duplex microstructure. × 200

Fig. 7

The pearlitic structure formed by annealing the 20 per cent platinum-molybdenum alloy for 165 hours at 1250°C. × 750

The pearlitic structure formed by annealing the 20 per cent platinum-molybdenum alloy for 165 hours at 1250°C. × 750

At lower temperatures a second phase separated from this terminal solid solution (Fig. 6) which in turn decomposed at temperatures below about 1300°C to yield the pearlitic microstructure shown in Fig. 7. X-ray diffraction showed that the high temperature duplex microstructure was composed of body centred cubic and cubic (β-tungsten) structures, the latter corresponding to the ε phase described by Rooksby. The low temperature duplex structure consisted of a body centred cubic and a hexagonal phase corresponding to that designated by Rooksby as δ.

The individual phases present in specimens quenched from temperatures above 1300°C were fully resolvable under the electron probe microanalyser, and their compositions were determined. The analytical results have been plotted in Fig. 8, which illustrates the very rapid increase in the solubility of platinum in molybdenum between 1400° and 1700°C, and the constancy of the high temperature ε phase composition over this region. The ε phase decomposes eutectoidally at 1325° ±25°C, according to the metallographic evidence obtained on the two alloys examined.

Fig. 8

Boundary curves for the molybdenum-rich terminal solid solution and the high temperature ε phase as determined by electron probe microanalysis of alloys in the duplex region

Boundary curves for the molybdenum-rich terminal solid solution and the high temperature ε phase as determined by electron probe microanalysis of alloys in the duplex region

Practical Significance of the High Temperature Phase Relationships


When attempts are made to use the desirable properties of platinum-clad molybdenum at temperatures above 1300°C failure tends to take place in a characteristic manner. Large distortions of the sheath begin to occur, giving the component a “blistered” appearance, and eventually the sheath cracks, so that catastrophic oxidation of the molybdenum can take place without hindrance. Such failures are rarely associated with the complete diffusion of molybdenum to the outer platinum surface.

From laboratory experience with the manufacture of test composites it has become quite clear that unless special precautions are taken it is difficult to maintain a coherent interface during annealing when the heat treatments are carried out above 1300°C, and that this difficulty is mainly due to high interface strains associated with the formation of the high temperature intermetallics in the diffusion zone. The formation of these phases could similarly account for the distortions observed in glass handling equipment used at high temperatures.

Further theoretical work on this and other refractory metal platinum systems which are potentially useful at high temperatures would thus be of considerable practical value to metallurgists and engineers concerned with plant design and development.

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References

  1. 1
    L. Dreibholz, Z. phys. Chem., 1924, 108, 5
  2. 2
    R. Hultgren and R. I. Jaffee, J. Appl. Phys., 1941, 12, 501
  3. 3
    E. Raub, Z. Metallk., 1954, 45, 23
  4. 4
    P. Greenfield and P. A. Beck, Trans. A.I.M.E., 1956, 206, 265
  5. 5
    H. Nishimura, Nippon Kinzoku Gakkai–Si, 1958, 22, 425
  6. 6
    A. G. Knapton, Planseeber., 1959, 7, 2
  7. 7
    K. Kirner, Metall, 1962, 16, ( 7 ), 672
  8. 8
    H. P. Rooksby and B. Lewis, J. Less-Common Metals, 1964, 6, 451
  9. 9
    A. G. Knapton, J. Inst. Metals, 1958 –59, 87, 28
 

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