On the constitution of the ternary system Al–Ni–Ti

Schuster, Julius C.; Pan, Zhu; Liu, Shuhong; Weitzer, F.; Du, Yong

doi:10.1016/j.intermet.2007.03.003

Cited by 75 publications

(49 citation statements)

References 12 publications

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“…[9] Various assessments are available for the Ti-Ni-Al system [3,12,13] and backed by new experimental data on alloys annealed at 900°C in wellcalibrated thermal environment; our previous results on the Section I: Basic and Applied Research isothermal section at 900°C [32] and on the Ti-Ni-Al Laves phase [26] are retained for the present work. The Ti-Fe-Ni isothermal section at 900°C from van Loo et al [44] was used.…”

Section: Ternary Subsystemsmentioning

confidence: 99%

“…Recent reviews for the subsystems of the Ti-Fe-Ni-Al quaternary provide such information. [1][2][3][4][5][6][7][8][9][10][11][12][13][14][15] However, on the extension from the ternary systems to the quaternary system, there are only few investigations available in literature. [16][17][18][19][20][21][22][23][24] Past efforts associated with the quaternary system include: (i) the relation between structure and magnetic properties of a magnetically semipermanent alloy with specific compositions Fe-(10-25)Ni- (3)(4)(5)Al-1Ti (wt.%), [16] Fe-18Ni-3.8 Al-1Ti (wt.%), [17] Fe-13.8Ni-7.0Al-1.7Ti (at.%), [18] and Fe-16.2Ni-3.1Al-1.13Ti (wt.%), [19] (ii) alloying effects on superplastic behavior for Ti-based alloys Ti-5Fe-xAl-yNi (x = 4-8, y = 0, 1, or 2) (wt.%), [22] (iii) phase relation between CsCl-type and Heusler phases within the NiAlTiNi-TiFe-FeAl section, [21] (iv) Partitioning behavior of alloying elements among the phases of c¢, g, b 1 , b 2 , and H in the Ni-Al-Ti base systems, [23] and (v) the effect of Ti additions on the microstructure of Ni-Al-Fe alloys.…”

Section: Introductionmentioning

confidence: 99%

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On the Quaternary System Ti-Fe-Ni-Al

Yan

Grytsiv

Rogl

et al. 2008

J Phs Eqil and Diff

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The homogeneity ranges of the Laves phases and phase relations concerning the Laves phases in the quaternary system Ti-Fe-Ni-Al at 900°C were defined by x-ray powder diffraction (XPD) data and electron probe microanalysis (EPMA). Although at higher temperatures the Laves phase forms a continuous solid solution, two separate homogeneity fields of TiFe 2 -based (denoted by k Fe ) and Ti(TiNiAl) 2 -based (denoted by k Ni ) Laves phases appear at 900°C. The relative locations of Laves phases, G phase, Heusler phase, and CsCl-type phase as well as the associated tie-tetrahedra were experimentally established in the quaternary for 900°C and presented in three-dimensional (3D) view. Furthermore, a partial isothermal section TiFe 2 -TiAl 2 -TiNi 2 was constructed, and a connectivity scheme, derived for equilibria involving Laves phases in the Ti-Fe-Ni-Al quaternary system at 900°C was derived. As a characteristic feature of the quaternary phase diagram, the solid solubility of fourth elements in both the TiFe 2 -based and Ti(NiAl) 2 -based Laves phases is limited at 900°C and is dependent on the ternary Laves phase composition. A maximum solubility of about 8 at.% Ni is reached for composition Ti 33.3 Fe 33.3 Al 33.4 . Structural details have been evaluated from powder x-ray and neutron diffraction data for (i) the Ti-Fe-Ni ternary and the Ti-Fe-Ni-Al quaternary Laves phases (MgZn 2 -type, space group: P6 3 /mmc) and (ii) the quaternary G phase. Atom site occupation behavior for all phases from the quaternary system corresponds to that of the ternary systems. For the quaternary Laves phase, Ti occupies the 4f site and additional Ti (for compositions higher than 33.3 at.%Ti) preferably enters the 6h site. Aluminum and (Fe,Ni) share the 6h and the 2a sites. The compositional dependence of unit cell dimensions, atomic coordinates, and interatomic distances for the Laves phases from the quaternary system is discussed. For the quaternary cubic G phase, a centrosymmetric as well as a noncentrosymmetric variety was observed depending on the composition: from combined x-ray and neutron powder diffraction measurements Ti 33.33 Fe 13.33 Ni 10.67 Al 42.67 was found to adopt the lower symmetry with space groupF " 43m.

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Section: Ternary Subsystemsmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

On the Quaternary System Ti-Fe-Ni-Al

Yan

Grytsiv

Rogl

et al. 2008

J Phs Eqil and Diff

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“…[6] The Al-Ni-Ti phase diagram has been reviewed recently, and some discrepancies and incompleteness were identified. [7] Thermodynamic modeling of the system could benefit from additional thermodynamic data especially with regard to the enthalpy of formation of compounds in the system.…”

Section: Introductionmentioning

confidence: 99%

Enthalpy of Formation in the Al-Ni-Ti System

Nash

Chen³

2009

J. Phase Equilib. Diffus.

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The Al-Ni-Ti ternary system forms the basis of several alloy systems of practical importance. This study was undertaken to provide additional experimental thermodynamic data for the modeling of the Al-Ni-Ti system. High-temperature direct reaction calorimetry has been used to determine the standard enthalpy of formation of several Al-Ni-Ti alloys. The stability of the L2 1 structure over the B2 structure at the stoichiometric composition of Ni 0.5 Al 0.25 Ti 0.25 was estimated from the enthalpy results to be 6.8 kJ/mol. The lattice parameters and melting temperatures of these compounds are also reported.

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“…Both the ternary systems of Ni-TiAl [38][39][40] and Fe-Ti-Al [41,42] show a prominent presence of ternary Heusler phases with L2 1 structure, i.e., Ni 2 TiAl and Fe 2 TiAl, respectively over a large solubility range in the respective phase diagrams. [38,40] Kainuma et al, [43] and more recently Yan et al, [44] reported detailed studies on the phase stability of the Ni-Fe-Ti-Al quarternary system.…”

Section: Ss-braze Alloy Interfacementioning

confidence: 99%

Microstructure and Interfacial Reactions During Active Metal Brazing of Stainless Steel to Titanium

Laik

Shirzadi

Tewari

et al. 2013

Metall Mater Trans A

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Microstructural evolution and interfacial reactions during active metal vacuum brazing of Ti (grade-2) and stainless steel (SS 304L) using a Ag-based alloy containing Cu, Ti, and Al was investigated. A Ni-depleted solid solution layer and a discontinuous layer of (Ni,Fe) 2 TiAl intermetallic compound formed on the SS surface and adjacent to the SS-braze alloy interface, respectively. Three parallel contiguous layers of intermetallic compounds, CuTi, AgTi, and (Ag,Cu)Ti 2 , formed at the Ti-braze alloy interface. The diffusion path for the reaction at this interface was established. Transmission electron microscopy revealed formation of nanocrystals of Ag-Cu alloy of size ranging between 20 and 30 nm in the unreacted braze alloy layer. The interdiffusion zone of b-Ti(Ag,Cu) solid solution, formed on the Ti side of the joint, showed eutectoid decomposition to lamellar colonies of a-Ti and internally twinned (Cu,Ag)Ti 2 intermetallic phase, with an orientation relationship between the two. Bend tests indicated that the failure in the joints occurred by formation and propagation of the crack mostly along the Tibraze alloy interface, through the (Ag,Cu)Ti 2 phase layer.

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On the constitution of the ternary system Al–Ni–Ti

Cited by 75 publications

References 12 publications

On the Quaternary System Ti-Fe-Ni-Al

On the Quaternary System Ti-Fe-Ni-Al

Enthalpy of Formation in the Al-Ni-Ti System

Microstructure and Interfacial Reactions During Active Metal Brazing of Stainless Steel to Titanium

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