Bulk glass formation and mechanical properties for Cu–Hf–Ti–M (M=B,Y) alloys

Figueroa, I.A.; Rawal, Ritesh; Stewart, P.S.B.; Carroll, P.A.; Davies, H.A.; Jones, H.; Todd, Iain

doi:10.1016/j.jnoncrysol.2006.12.068

Cited by 18 publications

(24 citation statements)

References 7 publications

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“…The liquidus temperature TL has its minimum value for the 20at%Ti alloy in Table 1, probably corresponding to a ternary eutectic system, it is because only this composition has single melting peak in the DTA trace [2]. Thus this is a dominating factor in determining that Trg has its maximum value at this composition clearly.…”

Section: Experimental Processes With Dsc Annealingmentioning

confidence: 91%

“…Table 1. Glass forming section thickness and thermal property for Cu60Hf40-XTiX (X=from 5 to 35) alloy series [2] After all, the aim of this research is also to clarify a quantitative evaluation in the structure relaxation processes focusing on the activation energy in Cu60Hf20Ti20 based amorphous alloys with high GFA series.…”

Section: Experimental Processes With Dsc Annealingmentioning

confidence: 99%

“…Activation energy for structural relaxation process in a metal type amorphous ternary and quaternary alloys, with cross sections of typically 0.03 mm x 2.0 mm, prepared by chill-block melt spinning has been investigated by Differential Scanning Calorimetry (DSC) with a cyclically heating technique [1,2,3]. Activation energies for structural relaxation with a spatial quantity in amorphous materials have been discussed by use of a total relaxed ratio function that depends on annealing temperature and time.…”

Section: Introductionmentioning

confidence: 99%

“…Particularly Cu has been shown to be good base element for bulk glass-forming alloy with fully glassy sections recently by use of die injection casting [2,3]. Binary Cu -(Zr or Hf) alloys have been found to form an amorphous phase over a wide composition range.…”

Section: Introductionmentioning

confidence: 99%

“…Binary Cu -(Zr or Hf) alloys have been found to form an amorphous phase over a wide composition range. However, addition of Ti in both these binary systems greatly increased the glass forming ability (GFA), with the critical diameter for fully amorphous rods being at least 4 mm for Cu60Zr30Ti10, Cu60Hf20Ti20 and Cu55Hf25Ti20 [2,3]. Meanwhile the understanding of the structural relaxation process is essential in the development of stability for amorphous alloys, as well as in establishing stable working temperature to avoid the degradation of strength.…”

Section: Introductionmentioning

confidence: 99%

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Numerical Solutions for Structural Relaxation of Amorphous Alloys Studied by Activation Energy Spectrum Model

Yamada¹

2013

Applications of Calorimetry in a Wide Context - Differential Scanning Calorimetry, Isothermal Titration Calorimetry and Microca

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Section: Experimental Processes With Dsc Annealingmentioning

confidence: 91%

Section: Experimental Processes With Dsc Annealingmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

See 3 more Smart Citations

Numerical Solutions for Structural Relaxation of Amorphous Alloys Studied by Activation Energy Spectrum Model

Yamada¹

2013

Applications of Calorimetry in a Wide Context - Differential Scanning Calorimetry, Isothermal Titration Calorimetry and Microca

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Formation and Thermal Stability of Cu‐Hf‐Ti‐M Glassy Alloys

et al. 2007

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Since 1995, Cu has been shown to be a good base element for bulk glass-forming alloys, with fully glassy sections up to 7 mm being reported. [1] For instance, Lin and Johnson [2] produced 4 mm thick glassy strips of Cu 47 Ti 34 Zr 11 Ni 8 alloy by copper die injection casting. The introduction of 1 at.% Si increased the critical thickness for glass formation to 7 mm. [1] Binary Cu -(Zr or Hf) alloys have been found to form an amorphous phase [3][4] over a wide composition range. However, addition of Ti in both these binary systems greatly increased the glass forming ability (GFA), [5][6][7][8] with the critical diameter for fully amorphous rods being at least 4 mm for Cu 60 Zr 30 Ti 10 , Cu 60 Hf 20 Ti 20 and Cu 55 Hf 25 Ti 20 . On the other hand, it has been shown that small additions of B and Y [7] and of Nb, Ta and Mo [9] reduce the GFA for Cu-Hf-Ti alloys.One of the empirical rules for high GFA in a metallic alloy is that the heat of formation from the constituent elements is negative. Nevertheless, although addition of alloying elements with positive enthalpy of solution should reduce the GFA, there have been some reports that the addition of elements with positive heats of mixing enhances GFA, [10][11][12][13] though Xu et al. [10] show that this occurs only when they decrease the melting temperature of the alloy. The objective of the present study was to investigate the effects of small concentrations of Al, Mo, Si and V on the GFA and thermal stability for Cu-Hf-Ti-based alloys.Cu-based alloy ingots of composition Cu 55-x Hf 25 Ti 20 M x (M = Al, Mn, Si, V, where v = 1, 2, 4 and 7 at.%) were prepared by argon arc melting mixtures of Cu (99.99 % pure), Hf (99.8 % pure), Ti (99.98 % pure), Al (99.99 % pure) Mn (99.99 % pure) Si (99.99 % pure) and V (99.98 % pure). The alloy compositions represent the nominal values but the weight losses in melting were negligible (< 0.1 %). The alloy ingots were inverted on the hearth and re-melted several times, to ensure compositional homogeneity. Conical alloy shapes, of length ∼ 50 mm and having a minimum diameter of 1 mm and a maximum of 10 mm, were produced by copper mould suction-casting within the argon arc furnace. [6] Additionally, ribbon samples of each alloy, with cross sections of typically 0.03 mm × 2.0 mm, were produced by chill-block melt spinning in a sealed argon atmosphere. The structures of the conical and ribbon samples were studied by XRD and the glass transition (T g ) and crystallisation (T x ) temperatures determined by DSC (using a Perkin Elmer DSC-7) at a heating rate of 0.33 K/s. The initial melting (T m ) and liquidus (T l ) temperatures were measured by DTA (Perkin Elmer DTA-7) at a heating rate of 0.33 K/s. Both, the DSC and the DTA instruments were calibrated at the respective heating rates using the known melting temperatures of pure metals. The measured T l corresponding to the completion of the melting transformation were adjusted to allow for thermal lag, using a correction factor determined earlier by Donald and Davies. [14] Initiall...

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