Bodaka and deals with ternary alloys of rare earths and germanium - their phase diagrams and crystal structures of intermediate phases. Chabot, Crystal structures and crystal chemistry of ternary rare earth transition metal borides, silicides and homologues 113. R Rogl, Phase equilibria in ternary and higher order systems with rare earth elements and boron 335 50.
E Rogl, Phase equilibria in ternary and higher order systems with rare earth elements and silicon 52.
The immiscibility gap that exists in the Ce-Li binary system extends to 17 at.% Ge in the ternary system. The immiscibility gap that exists in the Sm-Li binary system extends to 17 at.% Ge in the ternary system. The alloy was prepared by heating the elements in the stoichiometric ratio 1:2:1 in a Ta crucible under dry Ar to a temperature above 1000 K. The sample was annealed under unspecified conditions until only GdLiGe and excess Li were exposed by X-rays. were detected. analysis.
The immiscibility gap that exists in the H o-Li binary system extends to 17 at.% Ge in the ternary system.
Rare-earth-p element-germanium systems
The information on the interaction of the components in the E u - M g - G e system is due to Zmii et al. No phase diagram exists for the Nd - B - Ge e system, however the solubility of boron in the NdsGe3 compound has been investigated using X-ray diffraction (Mayer and Felner 1974). The only information on the Gd - B - G e system is due to Mayer and Felner (1974), who investigated the solubility of boron in the GdsGe3 compound by X-ray diffraction.
Solubility of boron in the DysGe3 compound was studied by X-ray methods (Mayer and Felner 1974).
TERNARY RARE-EARTH-GERMANIUM SYSTEMS 23
Samples were obtained by arc melting the correct amounts of pure components in an argon atmosphere (Ce, A1 and Ge: 99.99 mass%). Samples were obtained by arc melting the correct amounts of pure components in an argon atmosphere (Pr, A1 and Ge: 99.99 mass%). Samples were obtained by arc melting the correct amounts of pure components in an argon atmosphere (Dy, A1 and Ge: 99.99 mass%).
Samples were obtained by arc melting appropriate amounts of pure components in an argon atmosphere (Ho, A1 and Ge: 99.99 mass%).
TERNARY RARE-EARTH-GERMANIUM SYSTEMS 39
Crystallographic data for the t e m a r y compounds observed in the course of phase equilibrium studies in the S c - M n - G e system at 870 K are examined in table O. 1992) the crystal structure for the ScMn6Ge6 compound at t073 K . and confirmed the same structure type with similar lattice parameters. Crystallographic data for the ternary Sc--Ni-Ge compounds observed at 870 K are listed in table 9. The crystal structure for the Sc3Cu4Ge4 compound (1) was studied by Thirion et al.
The crystallographic features for the compound ScCuGe (2) (ZrNiAI species, a = 0.6515, c = 0.3972) reported by Kotur and Andrusyak (1984b) are in good agreement with those previously predicted by Dwight et al.
For details about sample preparation, see Sc-Ru-Ge. 1986a) investigated the crystal structure of the compound Sc4Rh6Ge19. The alloy was arc melted and annealed at 870 K. The purity of the starting materials was greater than 99.9 mass. For purity of starting materials, see YNi»Ge3, above. 1989) investigated the formation and crystal structure of.
Lanthanum-cobalt-germanium combinations have only been studied with respect to. the formation and crystal structure of compounds with different stoichiometries. The sample was prepared by a powder metallurgical reaction and annealed in an evacuated silica tube at 1173 K. 1989) investigated the formation and crystal structure of the LaCol_xGe2 compound by X-ray powder analysis of an arc fused alloy annealed at 870 K. The sample was melted in an induction oven. The crystal structure of the La6Co13Ge compound was reported by Weitzer et al.
1985b) reported on the X-ray powder diffraction study of the LaRhGe3 compound from the sample, which was prepared by heating the mixture of starting components (La 3N, Rh 4N, Ge 4N) in evacuated quartz tube at 1073 K. 1985b) reported on the X-ray powder diffraction study of The LaIrGe3 compound from a sample prepared by heating a mixture of starting components (La 3N, Ir 4N, Ge 4N) in an evacuated quartz tube at 1073 K. 1979) from X-ray powder diffraction of the induction melted sample which was annealed at 773 K for 1 week .
1985b) reported an X-ray powder diffraction study of the compound Ce3Ir4Ge13 from a sample prepared by heating a mixture of starting components (Ce 3N, Ir 4N, Ge 4N) in an evacuated quartz tube at 1073 K. The crystal structure was designed to accept the type Yb3Rh4Snl3 , a=0.9061. The sample was prepared by heating a mixture of powders of the starting components [Ce (3N), Ir (3N) and Ge (3N)] in a vacuum silicon tube at 1173 K. The existence of the CePtGe2 compound was not confirmed by Gribanov et. al. For sample preparation see CeRu2Ge2 under Ce-Ru-Ge. 1985b) reported an X-ray powder diffraction study of the compound PrRhGe3 from a sample prepared by heating a mixture of starting components (Pr 3N, Rh 4N, Ge 4N) in an evacuated quartz tube at 1073 K.
For the experimental procedure see La4Ir13Ge9 under La-Ir-Ge. 1985b) reported an X-ray powder diffraction study of the compound Pr3Ir4Ge13 from a sample prepared by heating a mixture of starting components (Pr 3N, Ir 4N, Ge 4N) in an evacuated quartz tube at 1073 K.
TERNARY RARE-EARTH-GERMANIUM SYSTEMS 89
For sample preparation, see Nd-V-Ge. 1994) observed the Nd117Cr52Ge112 compound during the study of the Nd-Cr-Ge isothermal section. The phase field distribution in the Nd-Mn-Ge system at 870 K is characterized by the formation of three ternary compounds: NdMn6Ge6 (1), NdMn2Ge2 (2) and NdMnxGe2 (3) according to Salamakha et al. The arc-fused buttons were annealed at 870 K for 2 weeks in vacuum-sealed quartz capsules and finally quenched by immersing the ampoules in cold water.
Two more ternary compounds are known from early investigations of ternary neodymium-iron-germanium combinations conducted by Felner and Schieber (1973) and Weitzer et al. Crystallographic data for the ternary phases of the Nd-Ni-Ge system are reported in table 20. Information on the phase equilibria in the Nd-Cu-Ge system (Fig. 62) is due to the work of Salamakha (1988) who X-ray phase analysis of argon arc molten ternary alloys; the samples were annealed in vacuum-sealed quartz ampoules at 870 K for.
No isothermal section is available for the ternary Nd-Zn-Ge system, but one ternary compound was observed and characterized by Rossi and Ferro (1996). The metals used in sample synthesis had a nominal purity of 99.9 mass% for neodymium, and 99.999 mass% for the other metals. Salamakha and Starodub (1991) were the first to investigate the phase relationships within the isothermal section at 870 K over the entire concentration range by X-ray powder analysis (fig. 63).
The phase relations in the Nd-Nb-Ge ternary system at 870 K are shown in fig. As determined by X-ray powder diffraction analysis of samples annealed at 870 K, phase equilibria revealed the absence of ternary compounds.
For sample preparation, see GdFeGe2 under Gd-Fe-Ge. 1985b) reported an X-ray powder diffraction study of the Gd3Rh4Gel3 compound of a sample prepared by heating mixture of starting components (La 3N, Ru 4N, Ge 4N) in an evacuated quartz tube at 1073 K. 1986b) from a sample prepared by a powder metallurgical reaction at 1173 K. The purity of the starting materials was greater than 99.9 mass%. 1984) observed the GdsIr4Gei0 compound with Sc»Co4Sil0-type structure from a sample obtained by heating a mixture of the starting components in an evacuated silica tube at 1073 K. 1986b) from a sample prepared by a powder metallurgical reaction at 1173 K was prepared. purity of the starting material was greater than 99.9 mass%. The existence and crystal structure of this compound was confirmed by Starodub (1988) from an arc-melted sample annealed at 870K. Apparently, this phase does not exist at 870 K. The phase diagram of the Tb-Nb-Ge system has not been established.
For sample preparation, see La2Ru3Ge» under La-Ru-Ge. 1985b) reported an X-ray powder diffraction study of the Tb3Rh4Ge13 compound from a sample prepared by heating a mixture of the starting components (Tb 3N, Rh 4N, Ge 4N) in an evacuated quartz tube at 1073 K. 1986b) from a sample prepared by powder metallurgical reaction at 1173 K. The purity of the starting materials was greater than 99.9% by mass. 1986b) from a sample prepared by a powder metallurgical reaction at 1173 K. The purity of the starting materials was greater than 99.9% by mass. The alloy was arc melted and annealed at 870 K. The purity of the starting materials was greater than .
The samples were prepared by a powder metallurgical reaction and annealed in an evacuated silicon tube at 1173 K. The crystal structure of I)y3Co4Gel3 (Yb3Rh4Snl3 type, a=0.8744; X-ray powder diffraction) was investigated by VentaJrini et al. For sample preparation see La2Ru3Ge5 under La-Ru-Ge. 1985b) reported an X-ray powder diffraction study of the compound Er3Rh4Ge13 from a sample prepared by heating a mixture of starting components (Er 3N, Rh 4N, Ge 4N) in an evacuated quartz tube at 1073 K. 1986b) from an alloy synthesized by a powder metallurgical reaction at 1173 K. The purity of the starting materials was greater than 99.9 wt.%. S A L A M A K H A et al. . powder diffraction) from a sample obtained by a powder metallurgical reaction at 1173 K. The phase diagram of the T m - N b - G e system has not been established.
For sample preparation, see La2Ru3Ge5 under La-Ru-Ge. 1985b) reported an X-ray powder diffraction study of the crystal structure of Tm3Rh4Gel3 from an alloy prepared by heating a mixture of the starting components (Tm 3N, Rh 4N, Ge 4N) in an evacuated quartz tube at 1073 K. 1986b ) of a sample prepared by a powder metallurgical reaction at 1173 K. The purity of the starting material was greater than 99.9 mass%. The alloy was synthesized by heating a mixture of powders of the constituent elements in an evacuated quartz tube at 1273 K. The alloy was obtained by a powder metallurgical reaction and annealed at 1073 K. No ternary phase diagram was established for the Tm-Ir not. -Ge system, but five ternary compounds have been characterized. The sample was prepared by heating a mixture of powders of the starting components (Tm 3N, Pt 3N, Ge 3N) in an evacuated silica tube at 1173 K. The only information about the interaction of components in the ternary T m - A u -Ge system is due to Pöttgen et al. 1996a) who observed and characterized the TmAuGe compound.
Apparently, this phase does not exist at 670 K. The alloys for investigation were prepared by arc melting.
