COMPOSITION DESIGN OF Fe-B-Si-Ta BULK AMORPHOUS ALLOYS BASED ON CLUSTER+ GLUE ATOM MODEL

doi:10.11900/0412.1961.2014.00615

Acta Metall Sin

2015, Vol. 51

Issue (8): 1017-1024 DOI: 10.11900/0412.1961.2014.00615

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COMPOSITION DESIGN OF Fe-B-Si-Ta BULK AMORPHOUS ALLOYS BASED ON CLUSTER+ GLUE ATOM MODEL

Yaoxiang GENG^1,²,Kaiming HAN^1,²,Yingmin WANG^1,²,Jianbing QIANG^1,²(

),Qing WANG^1,²,Chuang DONG¹,Guifeng ZHANG²,O TEGUS³,Peter HAÜSSLER^1,⁴

1 Key Lab of Materials Modification by Laser, Ion and Electron Beams, Ministry of Education, Dalian University of Technology, Dalian 116024
2 School of Materials Science and Engineering, Dalian University of Technology, Dalian 116024
3 Inner Mongolia Key Laboratory for Physics and Chemistry of Functional Materials, Inner Mongolia Normal University, Hohhot 010022
4 Physics Institute, Chemnitz University of Technology, Chemnitz 09107

Cite this article:

Yaoxiang GENG,Kaiming HAN,Yingmin WANG,Jianbing QIANG,Qing WANG,Chuang DONG,Guifeng ZHANG,O TEGUS,Peter HAÜSSLER. COMPOSITION DESIGN OF Fe-B-Si-Ta BULK AMORPHOUS ALLOYS BASED ON CLUSTER+ GLUE ATOM MODEL. Acta Metall Sin, 2015, 51(8): 1017-1024.

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Abstract

The structural and compositional features of amorphous alloys can be described by cluster-plus-glue atom model, which is an effective method for the composition design of amorphous alloys. In the Fe-B binary system, Fe₂B phase is an intermetallic phase related to Fe₈₃B₁₇ eutectic point. Under the framework of the highest radial number density and isolation principle, the local structure of Fe₂B phase is characterized by a B-centered Archimedean octahedral antiprism [B-B₂Fe₈] atomic cluster. Combined with the electron consistence criterion, the [B-B₂Fe₈]Fe (here the center and shell atoms are separated by a hyphen, a cluster is enclosed in square brackets, the glue atom is out square brackets) is then determined as an ideal cluster formula for Fe-B binary amorphous. To further enhance the glass-forming ability (GFA) of the alloy, the center B and shell Fe atoms in [B-B₂Fe₈]Fe are replaced with Si and Ta, respectively, due to their large negative enthalpy of mixing between Si-Fe and (B, Si)-Ta atomic pairs, and Fe-B-Si-Ta quaternary composition series, namely [Si-B₂Fe₈_-_xTa_x]Fe, are thus derived. The experimental results reveal that the bulk amorphous alloys with a diameter of 1.0 mm can be achieved for [Si-B₂Fe₈_-_xTa_x]Fe (x=0.4~0.7) compositions. Among them, [Si-B₂Fe_7.4Ta_0.6]Fe (i.e. Fe₇₀B_16.67Si_8.33Ta₅, atomic fraction, %) is the best glass former, its glass transition temperature T_g, supercooled liquid region ΔT_x and the reduced glass transition temperatures T_rg are 856 K, 33 K and 0.584, respectively. The Vickers hardness, saturation magnetization and coercivity of the [Si-B₂Fe_7.6Ta_0.4]Fe (i.e. Fe_71.67B_16.67Si_8.33Ta_3.33) amorphous alloy are measured to be 1117 HV, 1.37 T, and 3.0 A/m, respectively.

Key words: cluster-plus-glue atom model cluster formula Fe-B-Si-Ta bulk amorphous alloy magnetism

Received: 07 November 2014

Fund: Supported by National Natural Science Foundation of China (Nos.51131002 and 51041011), Fundamental Research Funds for the Central Universities (No.DUT13ZD102), Scientific and Technological Development Foundation of China Academy of Engineering Physics (No.2013A0301015), National Defense Basic Scientific Research Project (No.B1520133007) and National Magnetic Confinement Fusion Science Program (No.2013GB107003)

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	Articles by authors
	Yaoxiang GENG
	Kaiming HAN
	Yingmin WANG
	Jianbing QIANG
	Qing WANG
	Chuang DONG
	Guifeng ZHANG
	O TEGUS
	Peter HAÜSSLER

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https://www.ams.org.cn/EN/10.11900/0412.1961.2014.00615 OR https://www.ams.org.cn/EN/Y2015/V51/I8/1017

Fig.1 Radial number density (r_A) distribution around B and Fe atoms in Fe₂B phase (r—distance from center to shell in cluster)

Fig.2 Models of Fe-centered [Fe-Fe₁₁B₄] cluster (a) and B-centered Archimedean octahedral antiprism [B-B₂Fe₈] cluster (b) in Fe₂B phase

Table 1 The cluster formulas, corresponding chemical compositions, mass densities (r), average atomic weight (M), average cluster radius (r₁) and number of valence electrons per unit formula ratios (e/u) of Fe-B amorphous alloys

Fig.3 XRD spectra of [Si-B₂Fe₈_-_xTa_x]Fe ribbons (a), 1.0 mm rods (b) and 1.5 mm rods (c) (Arrows in Fig.3a show that the diffraction angles (2q) of the principal diffusion peak gradually decrease with the increase of Ta contents)

Fig.4 OM images of cross section of the as-cast [Si-B₂Fe₈_-_xTa_x]Fe alloy rods with x=0.4, diameter=1 mm (a), x=0.5, diameter=1.5 mm (b), x=0.6, diameter=1.5 mm (c) and x=0.7, diameter=1.5 mm (d)

Fig.5 DSC (a) and DTA (b) curves of [Si-B₂Fe₈_-_xTa_x]Fe ribbon alloys (Arrows in Fig.5a show the Curie temperature (T_c) and glass transition temperature (T_g), arrows in Fig.5c show the melting temperature (T_m) and liquidus temperature (T_l), T—temperature)

Fig.6 Variations of supercooled liquid temperature spans (ΔT_x) and reduced glass transition temperature (T_rg) against Ta contents in [Si-B₂Fe₈_-_xTa_x]Fe amorphous alloys

Table 2 The Cluster formulas, corresponding chemical compositions, critical diameters (D_cr), T_g, crystallization temperature (T_x), ΔT_x, T_l, T_rg, Vickers hardness (H_V), and T_c of the Fe-B-Si-Ta amorphous alloys

Fig.7 Magnetization (a) and magnetic hysteresis loops (b) for [Si-B₂Fe₈_-_xTa_x]Fe (x=0, 0.4 and 0.6) amorphous ribbons (B_s—saturation magnetization, H—magnetic field, m₀—permeability of vacuum)

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