Thermodynamic description of the Mg–Nd–Zn ternary system

Qi, Haiying; Huang, Guanghui; Hong, Byungyou; Xu, Guanglong; Liu, L.B.; Jin, Zhanpeng

doi:10.1016/j.jallcom.2010.07.056

Cited by 42 publications

(14 citation statements)

References 27 publications

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“…The current study showed different phase relations than those reported by Qi et al [8], Drits et al [11], and Kinzhibalo et al [13] at 300 °C. However, the phase relations near the Mg-rich corner are consistent with Huang et al [1] except for the presence of the liquid phase, and consistent with Zhang et al [17] except for the presence of τ4 at 300 °C.…”

Section: Mg-nd-zn Isothermal Section At 300 °Ccontrasting

confidence: 96%

“…In addition, five three-phase regions, τ2+τ3+α-Mg, τ2+τ1+α-Mg, τ2+τ3+τ4, τ2+τ1+τ4, and α-Mg+τ1+L, were identified [1]. More recently, Qi et al [8] provided a thermodynamic description of the Mg-Nd-Zn system using the CALPHAD approach. Four stable ternary compounds, taken from the literature, were considered in their model [8].…”

Section: Literature Reviewmentioning

confidence: 99%

“…More recently, Qi et al [8] provided a thermodynamic description of the Mg-Nd-Zn system using the CALPHAD approach. Four stable ternary compounds, taken from the literature, were considered in their model [8]. These compounds are τ1 (Mg7NdZn12), τ2 (Mg7Nd2Zn11), τ3 (Mg6NdZn3), and τ4 (Mg6Nd3Zn11).…”

Section: Literature Reviewmentioning

confidence: 99%

“…Addition of neodymium to magnesium-based alloys results in improving their hardness and strength after an age hardening treatment. This can be attributed to the formation of fine-scaled solute-rich regions, Guinier-Preston zones (GP zones), in the Mg matrix [8]. On the other hand, the Nd-Zn binary phase diagram [9] shows the formation of a series of stable intermetallic compounds with high melting temperatures, which may result in improving the creep behavior of Mg alloys.…”

Section: Introductionmentioning

confidence: 99%

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Experimental Investigation of the Mg-Nd-Zn Isothermal Section at 300 °C

Mostafa¹,

Medraj²,

Chen³

2015

Metals

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Abstract:The Mg-Nd-Zn isothermal section at 300 °C was established in the full composition range using diffusion couples and equilibrated key alloys. Microstructural characterization was carried out using WDS, XRD, and metallographic methods. The homogeneity ranges of the binary and ternary compounds were determined by WDS analysis. Six ternary compounds were observed in the Mg-Nd-Zn system at 300 °C . These are: τ1 (Nd5Mg21+xZn45−x; 0 ≤ x ≤ 4), τ2 (Nd5Mg3+yZn25−y; 0 ≤ y ≤ 1), τ3 (NdMg1+zZn2−z; 0 ≤ z ≤ 0.44), τ4 (Mg40Nd5Zn55), τ5 (Mg22-23.5Nd15.5-17.5Zn59.1-61.8), and τ6 (Nd2(Mg,Zn)23). τ5 was found to have a homogeneity range of 22.0-23.5 atom % Mg, 15.5-17.6 atom % Nd and 59.1-61.8 atom % Zn and τ6 was found to have 54.1-61.3 atom % Mg at a constant Nd of 8.0 atom %. The ternary solubility of Zn in Mg-Nd compounds was found to increase with the decrease in Mg concentration. Accordingly, (Mg41Nd5) was found to have an extended solubility of 3.1 atom % Zn, whereas (Mg3Nd) was found to have 30.0 atom % Zn. MgNd was found to have a complete substitution of Mg by Zn. The maximum solid solubility of Zn in α-Mg was measured as 4.8 atom % Zn.

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Section: Mg-nd-zn Isothermal Section At 300 °Ccontrasting

confidence: 96%

Section: Literature Reviewmentioning

confidence: 99%

Section: Literature Reviewmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

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Experimental Investigation of the Mg-Nd-Zn Isothermal Section at 300 °C

Mostafa¹,

Medraj²,

Chen³

2015

Metals

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“…The structures of the equilibrium intermetallic phases at the Mg-rich side of the Mg-Nd-Zn or Mg-CeZn ternary phase diagram have so far not been unambiguously established. [158][159][160][161] Therefore, it is difficult to know whether the Mg 3 Nd is an equilibrium phase at the Mg-rich side of the Mg-Nd-Zn alloys and, if so, whether c is the Mg 3 Nd phase.…”

Section: Mg-nd-zn and Mg-ce-zn Alloysmentioning

confidence: 99%

Precipitation and Hardening in Magnesium Alloys

Nie

2012

Metall Mater Trans A

1,396

519

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Magnesium alloys have received an increasing interest in the past 12 years for potential applications in the automotive, aircraft, aerospace, and electronic industries. Many of these alloys are strong because of solid-state precipitates that are produced by an age-hardening process. Although some strength improvements of existing magnesium alloys have been made and some novel alloys with improved strength have been developed, the strength level that has been achieved so far is still substantially lower than that obtained in counterpart aluminum alloys. Further improvements in the alloy strength require a better understanding of the structure, morphology, orientation of precipitates, effects of precipitate morphology, and orientation on the strengthening and microstructural factors that are important in controlling the nucleation and growth of these precipitates. In this review, precipitation in most precipitation-hardenable magnesium alloys is reviewed, and its relationship with strengthening is examined. It is demonstrated that the precipitation phenomena in these alloys, especially in the very early stage of the precipitation process, are still far from being well understood, and many fundamental issues remain unsolved even after some extensive and concerted efforts made in the past 12 years. The challenges associated with precipitation hardening and age hardening are identified and discussed, and guidelines are outlined for the rational design and development of higher strength, and ultimately ultrahigh strength, magnesium alloys via precipitation hardening.

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