Thermodynamic description on the miscibility gap of the Mg-based solid solution in the Mg–Zn, Mg–Nd and Mg–Zn–Nd systems

Niu, Chunju; Liu, Miao; Li, Changrong; Du, Zhenmin; Guo, Cuiping

doi:10.1016/j.calphad.2010.07.010

Cited by 22 publications

(7 citation statements)

References 17 publications

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“…4. This is in full agreement with Calphad assessments performed so far: there is a large number of systems known with a high-T artifact due to the linear model [10][11][12][13][14], while there is no system known so far with a low-T artifact of the exponential model among the systems studied by full Calphad assessment and properly giving the resulting data [23][24][25][26][27][28][29][30][31][32][33][34][35][36][37][38][39][40][41] (see Table 6). Based on this, the statement that the exponential model is not used as it might lead to a low-T artifact, and therefore instead a linear model is used [42] is not a wise strategy of Calphad assessment.…”

supporting

confidence: 87%

On the abilities and limitations of the linear, exponential and combined models to describe the temperature dependence of the excess Gibbs energy of solutions

Kaptay

2014

Calphad

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supporting

confidence: 87%

On the abilities and limitations of the linear, exponential and combined models to describe the temperature dependence of the excess Gibbs energy of solutions

Kaptay

2014

Calphad

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“…This equation was an answer to the problem raised in 2001 by Chen et al [14] on the appearance of artificial inverted miscibility gaps in many calculated phase diagrams. This equation has been applied successfully to the thermodynamic optimization of the Zn-Zr, [15] Ru-Zr, [16] Ru-Ti, [17] Cr-Ge, [18] Mg-Si, [19] Al-Er, [20] Gd-Tl, [21] Mg-Zn, Mg-Nd, Mg-ZnNd, [22] Co-Gd, [23] and Zr-Si-N [24] systems. Neither hightemperature nor low-temperature artifacts appeared in these 12 fully optimized systems, despite the conclusion based on a simplified analysis [25] (for further discussion, see .…”

Section: Introductionmentioning

confidence: 96%

On the Tendency of Solutions to Tend Toward Ideal Solutions at High Temperatures

Kaptay

2011

Metall Mater Trans A

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The rule of Lupis and Elliott (LE rule) proposed for the first time in 1966 is reformulated in this article as, ''Real solid, liquid and gaseous solutions (and pure gases) gradually approach the state of an ideal solution (perfect gas) as temperature increases at any fixed pressure and composition.'' This rule is rationalized through the heat expansion of phases and loss of any interaction with increased separation between the atoms. It is shown that the rule is valid only if the standard state is selected properly, i.e., if mixing does not involve any hidden phase changes, such as melting. It is shown that the necessary and sufficient practical conditions to obey the LE rule is the equality of signs of the heat of mixing and excess entropy of mixing and the nonequality of signs of heat of mixing and excess heat capacity of mixing of the same solution. It is shown that these two conditions are fulfilled for most of the experimentally measured high-temperature solutions. The LE rule is compared with the existing laws of thermodynamics. It is shown that the LE rule can be considered as a potential fourth law of materials thermodynamics.

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“…However, these peaks cannot match that of Sn–Nd, Mg–Nd and Mg–Zn–Nd compounds. 20–22 Zhao et al . and Gorney and Kataman 23–25 have investigated Mg–Zn–Mn–Sn–Y alloys and proposed that the diffraction peaks of MgSnY phase locate between 20° and 40° in the XRD patterns.…”

Section: Resultsmentioning

confidence: 99%

“…However, these peaks cannot match that of Sn-Nd, Mg-Nd and Mg-Zn-Nd compounds. [20][21][22] Zhao et al and Gorney and Kataman [23][24][25] have investigated Mg-Zn-Mn-Sn-Y alloys and proposed that the diffraction peaks of MgSnY phase locate between 20°and 40°in the XRD patterns. Wang et al 26 have reported that MgSnNd phase formed in the Mg-(1.65-11.52) wt-%Sn-2 wt-%Nd alloy, and its characteristic peaks match the new peaks perfect.…”

Section: Microstructuresmentioning

confidence: 99%

Thermodynamic analysis of the formation reaction of second phases in Mg–Zn–Mn–Sn–Nd alloys

Xing

Huang

et al. 2016

Materials Science and Technology

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The thermodynamic characteristics and solidification sequence of Mg-6Zn-1Mn-4Sn-xNd (x = 0.5, 1.0, 1.0, wt-%, ZMT614-xNd) alloys were investigated using CALPHAD, Miedema model, differential scanning calorimetry and transmission electron microscopy (TEM) analysis. The results revealed that the as-cast ZMT614-Nd alloys consisted of α-Mg, Mn, Mg 7 Zn 3 , Mg 2 Sn and MgSnNd phases. Owing to its higher phase transition temperature and lower formation enthalpy, MgSnNd phase formed first during the casting process. The formation of MgSnNd phase consumed all Nd elements, which restrained the formation of other Nd-containing phases. As a result, the solidification sequence of ZMT614-1.5Nd alloy was α-Mg → MgSnNd → Mn → Mg 2 Sn → Mg 7 Zn 3 . TEM analysis suggested that the MgSnNd phase had a low-symmetry crystal structure.

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Thermodynamic description on the miscibility gap of the Mg-based solid solution in the Mg–Zn, Mg–Nd and Mg–Zn–Nd systems

Cited by 22 publications

References 17 publications

On the abilities and limitations of the linear, exponential and combined models to describe the temperature dependence of the excess Gibbs energy of solutions

On the abilities and limitations of the linear, exponential and combined models to describe the temperature dependence of the excess Gibbs energy of solutions

On the Tendency of Solutions to Tend Toward Ideal Solutions at High Temperatures

Thermodynamic analysis of the formation reaction of second phases in Mg–Zn–Mn–Sn–Nd alloys

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