The Cu−Ge (Copper-Germanium) system

Olesinski, R. W.; Abbaschian, G. J.

doi:10.1007/bf02874979

Cited by 21 publications

(24 citation statements)

References 28 publications

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“…The available crystallographic data and phase equilibria of the Cu-Ge binary system in the published literature up to 1980 had been reviewed critically by Olesinski and Abbaschian [15]. The liquidus of the Cu-Ge phase diagram was measured firstly by Schwarz and Elstner [16] and afterwards by Reynolds and Hume-Rothery [17] using thermal analysis.…”

Section: Phase Diagram Datamentioning

confidence: 99%

Thermodynamic assessment of the Cu–Ge binary system

Wang

Jin

Leinenbach

et al. 2010

Journal of Alloys and Compounds

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Section: Phase Diagram Datamentioning

confidence: 99%

Thermodynamic assessment of the Cu–Ge binary system

Wang

Jin

Leinenbach

et al. 2010

Journal of Alloys and Compounds

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“…pct Ge) [8] shown in Figure 1 indicates that the f-phase fraction saturation level, f s is approximately the same for all isothermal temperatures employed in this study [i.e., 573 K, 613 K, and 653 K (300°C, 340°C, and 380°C)] and equals 0.68.…”

Section: Growth Modementioning

confidence: 70%

“…Solution annealing at 1023 K (750°C) and ice-water quenching was used to produce supersaturated a-Cu(Ge) solid solution specimens that under thermodynamic equilibrium are composed of f-phase and a-Cu(Ge) (shown by the red dashed line), reproduced using data from Ref. [8] (Color figure online). integrated at constant 2h along the Euler w-angle range from À111 to À69 deg.…”

Section: B In Situ and Ex Situ Xrd; Isothermal Annealing Experimentsmentioning

confidence: 99%

“…[1] In the Cu(Ge) system, the hcp product phase is called f-phase. The precipitation of the f-phase from supersaturated Cu(Ge) solid solutions complies with the same crystallographic orientation relationship as holds for the fcc fi hcp phase transformations observed in Co, Ag-Al, etc., i.e.,ð11 1Þa==ð0001Þf; ½ 110 a==½11 20 f. [1,2,[4][5][6] In contrast with the allotropic fcc fi hcp phase transformation occurring in Co, [7] the transformation in the Cu-Ge system is associated with compositional changes [1,8] (cf. Figure 1) and therefore the transformation mechanism is an intermediate class of a diffusionless, displacive, martensitic fcc fi hcp phase transformation and a diffusional phase transformation: Ge must diffuse to the f-phase nucleation sites and/or the growing f-phase plates to establish the f-phase composition.…”

Section: Introductionmentioning

confidence: 99%

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Kinetics of the fcc → hcp Phase Transformation in Cu-Ge Solid Solutions Upon Isothermal Aging

Polatidis

Zotov

Bischoff

et al. 2017

Metall Mater Trans A

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The kinetics of the f-phase formation from a supersaturated a-Cu(Ge) solid solution (i.e., transformation from the fcc crystal structure to the hcp crystal structure) containing 10.8 at. pct Ge [at isothermal temperatures of 573 K, 613 K, and 653 K (300°C, 340°C, and 380°C)] were studied by X-ray diffraction (XRD) for phase fraction determination. Both in situ and ex situ annealing experiments were performed. The transformation kinetics were modeled on the basis of a versatile modular model. The transformation kinetics complied with a site-saturation nucleation mode and strongly anisotropic interface-controlled growth mode in association with a corresponding impingement mode: diffusion of Ge (towards the stacking faults, SFs) does not control the transformation rate. Transmission electron microscopy (TEM) investigations showed that segregation of Ge at the stacking faults (SFs) takes place (relatively fast) prior to the structural transformation (fcc fi hcp).

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“…The copper-rich side of the Cu-Ge equilibrium phase diagram 10) is shown in Fig. 1, which indicates that the peritectic reaction, Fig.…”

Section: Introductionmentioning

confidence: 99%

Microstructures of Cu-Ge Alloy Rods Pulled from a Hyperperitectic Melt by the Czochralski Method

Imashimizu

Watanabé

2003

Mater. Trans.

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Cu-Ge alloy rods were pulled from a hyperperitectic melt at three kinds of pulling rates while the melt temperatures were lowered at controlled rates, respectively by the Czochralski method. The relationship between the pulling rate and the Ge concentration in the phase that solidified first from the melt is approximated by the relation derived from the BPS expression for the effective distribution coefficient. A group of peritectic grains is formed subsequent to the initial growth of crystal in the rods pulled at some rates. Growth of the grains is followed by growth of phase, resulting in the formation of alternating structures of the primary and the peritectic which is accompanied by a simultaneous variation in rod thickness. This appears repeatedly at short intervals along the rod when it is pulled at a high rate. It is concluded that the alternating structures of phase and peritectic grains are formed by a peritectic solidification of Ge-rich melt at the cell boundary that develops on a constitutionally supercooled solid-liquid interface, and that their cessation is due to a decrease in Ge concentration of the liquid at the interface, with subsequent growth of the phase.

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The Cu−Ge (Copper-Germanium) system

Cited by 21 publications

References 28 publications

Thermodynamic assessment of the Cu–Ge binary system

Thermodynamic assessment of the Cu–Ge binary system

Kinetics of the fcc → hcp Phase Transformation in Cu-Ge Solid Solutions Upon Isothermal Aging

Microstructures of Cu-Ge Alloy Rods Pulled from a Hyperperitectic Melt by the Czochralski Method

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