Mixed Phase Alloy Research Articles

Synthesis of cobalt-rich alloys with high saturation magnetization: A novel synthetic approach by hydrazine reduction method

Abstract Cobalt-rich alloys of various compositions (Co33Fe33Ni33, Co40Fe40Ni20, Co50Fe25Ni25 and Co60Fe20Ni20) were synthesized from their respective precursor salts using a novel hydrazine reduction method. The synthesized nanosized powders were characterized using X-ray diffraction (XRD), scanning electron microscopy (SEM), and vibrating sample magnetometer (VSM) techniques. XRD phase analysis results revealed that the Co33Fe33Ni33 alloy was formed with a pure FCC phase. Whereas, Co40Fe40Ni20, Co50Fe25Ni25 and Co60Fe20Ni20 alloys were composed of both FCC and BCC phases. The average particle size of the alloys was estimated to be in the range of 107–280 nm. The synthesized cobalt-rich alloys exhibited ferromagnetic properties at room temperature with a high saturation magnetization value up to 138 emu/g. The mixed phase Co40Fe40Ni20 alloy showed higher saturation magnetization and higher coercivity as compared to the other alloy compositions. In mixed phase alloys, the dominance of the BCC phase over the FCC phase seems to has resulted in the enhancement of the saturation magnetization value. The obtained results indicate that the hydrazine reduction method was effective in synthesizing cobalt-rich alloys with excellent soft magnetic properties.

Effect of Ti/Cr content on the microstructures and hydrogen storage properties of Laves phase-related body-centered-cubic solid solution alloys

A series of BCC/C14 mixed phase alloys with the chemical composition of Ti13.6+xZr2.1V44Cr13.2−xMn6.9Fe2.7Co1.4Ni15.7Al0.3, x=0, 2, 4, 6, 8, 10, and 12, was fabricated, and their structural, gaseous phase and electrochemical hydrogen storage properties were studied. Raising the maximum pressure for measuring the gaseous hydrogen storage capacity allowed these alloys to reach full activation, and the maximum discharge capacities ranged from 375 to 463mAhg−1. As the Ti/Cr ratio in the alloy composition increased, the maximum gaseous hydrogen storage capacity improved due to the expansion in both BCC and C14 unit cells. However, reversibility decreased due to the higher stability of the hydride phase, as indicated by the lower equilibrium pressures measured for these alloys. As with most other metal hydride alloys, the electrochemical capacities measured at 50 and 4mAg−1 fell between the boundaries set by the maximum and reversible gaseous hydrogen storage capacities. The poorer high-rate dischargeability observed with higher Ti/Cr ratios was attributed to the lower surface exchange current (less catalytic). Two other negative impacts observed with higher Ti/Cr ratios in the alloy composition are poorer cycle stability and lower open-circuit voltage.

Novel processing of iron–manganese alloy-based biomaterials by inkjet 3-D printing

The present work provides an assessment of 3-D printed iron–manganese biodegradable scaffolds as a bone scaffold material. Iron-based alloys have been investigated due to their high strength and ability to slowly corrode. Current fabrications of Fe-based materials generate raw material which must be machined into their desired form. By using inkjet 3-D printing, a technique which generates complex, customizable parts from powders mechanically milled Fe–30Mn (wt.%) powder was directly processed into scaffolds. The 3-D printed parts maintained an open porosity of 36.3% and formed a mixed phase alloy of martensitic ε and austenitic γ phases. Electrochemical corrosion tests showed the 3-D printed Fe–Mn to desirably corrode significantly more rapidly than pure iron. The scaffolds exhibited similar tensile mechanical properties to natural bone, which may reduce the risk of stress shielding. Cell viability testing of MC3T3-E1 pre-osteoblast cells seeded directly onto the Fe–Mn scaffolds using the live/dead assay and with cells cultured in the presence of the scaffolds’ degradation products demonstrated good in vitro cytocompatibility compared to tissue culture plastic. Cell infiltration into the open pores of the 3-D printed scaffolds was also observed. Based on this preliminary study, we believe that 3-D printed Fe–Mn alloy is a promising material for craniofacial biomaterial applications, and represents an opportunity for other biodegradable metals to be fabricated using this unique method.

Determination of miscibility in MgO-ZnO nanocrystal alloys by x-ray absorption spectroscopy

The local structure of MgxZn1−xO nanocrystals is studied using synchrotron x-ray absorption near edge structures (XANES) over the full range of composition, from x = 0 to 1. Mg and Zn K-edges XANES measurements allow us to selectively study the local environments around Mg and Zn atoms in these nanocrystalline samples. Our results indicate that, for MgO-ZnO alloys, Zn is highly miscible in the rocksalt domain (i.e., up to ∼50 at. %) while the miscibility of Mg in the wurtzite domain is much less but is still substantial (i.e., up to ∼20 at. %). The simulated XANES spectra, based on first principles methods, are consistent with the observed spectra, confirming our finding. Because it is short-ranged and element-specific, the technique is useful for local structure and crystal phase determination of nanostructures, quantum dots, and mixed-phase alloys in general.

Structure and mechanical properties of Mg 85Cu 5Zn 5Y 5 amorphous alloy containing nanoscale particles

The application of melt-spinning process of Mg 85Cu 5Zn 5Y 5 alloy was found to cause the formation of a mixed structure consisting of nanoscale crystalline particles embedded in an amorphous matrix. The Mg 85Cu 5Zn 5Y 5 (at.%) alloy has a mixed structure consisting of amorphous+hcp-Mg in the as-quenched state and amorphous+hcp-Mg+Mg 24Y 5 in an annealed state at 544 K for 300 s. The crystallization of the mixed phase alloy occurs through two stages of Am.(amorphous)→Am.+hcp-Mg→hcp-Mg+Mg 24Y 5. The particle size is as small as 10–30 nm in the as-quenched state and 20–40 nm in the annealed state, respectively. The tensile strength for Mg 85Cu 5Zn 5Y 5 alloy at 298 K is 467 MPa, being nearly twice as high as that (242 MPa) for a conventional crystalline AZ91(Mg–9wt.%Al–1wt.%Zn) alloy prepared at the same melt-spinning condition. Both of the ribbons exhibit good bending ductility. The high mechanical strength of the Mg 85Cu 5Zn 5Y 5 alloy is presumably due to the formation of the fine mixed structure consisting of nanoscale particles embedded in the amorphous matrix. These data allow us to expect the future progress as a new type of high specific strength material which can be fabricated with industrialization method.

Thermal and mechanical properties of amorphous Zr 65Al 7.5Ni 10Cu 12.5Ag 5 alloy containing nanocrystalline compound particles

The thermal and mechanical properties of an amorphous Zr 65Al 7.5Ni 10Cu 12.5Ag 5 alloy containing nanocrystalline compound phase were investigated. The Zr 3Al 2 phase with a spherical shape has a fine size of about 20 nm and is dispersed homogeneously at an interparticle spacing of about 30 nm in an amorphous matrix. The crystallization onset temperature and supercooled liquid regions decrease significantly with an increasing precipitation amount of Zr 3Al 2 phase, indicating an enhancement of thermal instability. This instability is presumably due to the change of the bonding nature among constituent atoms. The maximum tensile fracture strength (2070 MPa) of this mixed phase alloy is much higher than that (1200 MPa) for the amorphous single phase alloy with the same composition. Meanwhile, the good bending ductility of this alloy remains unchanged. Then, the fracture mode in the maximum tensile fracture strength was the shear type among the maximum shear plane. The significant increase of the tensile fracture strength is possibly due to the role of the nanoscale Zr 3Al 2 particles as an effective barrier to suppress shear sliding of the amorphous matrix.

Mechanical properties of Zr-based bulk glassy alloys containing nanoscale compound particles

For the last decade, bulk glassy alloys have been developed in a number of multicomponent alloy systems and have already gained practical applications. Although the bulk glassy alloys in Zr-based systems have high strength and good toughness, it has been found that the addition of special elements to the Zr-based glassy alloys causes the formation of a nanoscale mixed structure consisting of nanoscale intermetallic particles embedded in a glassy matrix and the mixed phase alloys exhibit higher mechanical strength and larger elongation as compared with the corresponding glassy single phase alloys. In particular, the bulk nanoscale mixed phase alloys in the Zr–Al–Ni–Cu–Nb system produced by squeeze casting exhibit extremely high bending flexural strength of 4400 MPa without fracture during the three point bending test. The mechanism for the formation of the nanoscale mixed structure for the alloys containing special additional elements as well as the reason for the remarkable improvement in the mechanical properties has been discussed on the basis of experimental results obtained by high-resolution TEM, nanobeam EDX spectroscopy, atom probe FIM and small angle X-ray scattering, in addition to DSC, ordinary TEM and X-ray diffraction.

Bulk amorphous FC20 (Fe–C–Si) alloys with small amounts of B and their crystallized structure and mechanical properties

The addition of a small amount (0.4 mass%) of B to a commercial FC20 cast iron was found to cause the formation of an amorphous phase in melt-spun ribbon and cast cylinders with a diameter of up to 0.5 mm. The structure of a melt-spun B-free FC20 alloy consisted of α-Fe, γ-Fe and Fe 3C. The effectiveness of additional B is presumably due to the generation of attractive bonding nature among the constituent elements. The amorphous alloy ribbon exhibits a high tensile strength of 3480 MPa and good bending ductility. The annealing causes the formation of an amorphous phase containing α-Fe particles with a size of about 30 nm. The mixed phase alloy exhibits an improved tensile strength of 3800 MPa without detriment to good ductility. With further increasing temperature, the mixed amorphous and α-Fe structure changes to α-Fe+Fe 3C+graphite through the metastable structure of α-Fe+Fe 3C. The structure after annealing for 900 s at 1200 K has fine grain sizes of about 0.5 μm for α-Fe, 0.3 μm for Fe 3C and 1 μm for graphite. The graphite-containing alloy exhibits high tensile strength of 1200–2000 MPa and large elongation of 5–13%. The high tensile strength and good ductility were also obtained for the 0.5 mm cylinder annealed at 1200 K. The good mechanical properties are due to the combination of fine subdivision of crack initiation sites by the homogeneous dispersion of small graphite particles and the dispersion strengthening of Fe 3C particles against the deformation of the α-Fe phase. The synthesis of the finely mixed α-Fe+Fe 3C+graphite alloys having good mechanical properties by crystallization of the new amorphous alloy in the melt-spun ribbon and cast cylinder forms is encouraging for the future development of a new Fe-based high-strength and high-ductility material.

Formation, Thermal Stability and Mechanical Properties of New Amorphous Al<SUB>89</SUB>Fe<SUB>10</SUB>Zr<SUB>1</SUB> Alloy

A new amorphous alloy with high tensile strength and good bending ductility was fabricated from a melt-spun Al 89 Fe 10 Zr 1 alloy without the lanthanide (Ln) element. The Al content for glass formation is believed to be the highest in the Ln-free Al-based alloys. The as-quenched phase changes to a mixed structure of amorphous and fcc-Al phases with decreasing Fe content to 7-9 at%, and the particle size of the Al phase is 40 nm at 7%Fe, 10 nm at 8%Fe and 5 nm at 9%Fe. The mixed phase alloys also have good bending ductility. The tensile fracture strength (σ f ) is 1050 MPa for the amorphous Al 89 Fe 10 Zr 1 alloy and decreases to 720-1000 MPa for the mixed phase alloys with 7 to 9%Fe concentrations. The amorphous alloy crystallizes by two-stage reactions of Am→Am+Al→Al+Al 3 Zr+Al 13 Fe 4 and the onset temperature of each exothermic reaction is 460 and 650 K. The σ f of the amorphous alloy increases to 1220 MPa without detriment to good ductile nature by the precipitation of about 20 vol% Al phase. The achievement of high σ f combined with good bending ductility in the Ln-free Al-Fe-Zr alloys with the high Al concentration of about 90% is important as a new basic alloy system to produce a high-strength Al-based alloy with low specific weight and inexpensiveness.

Mechanical properties of Al based alloys containing quasi-crystalline phase as a main component

The application of high-pressure Ar atomization to Al-Mn-TM and Al-Cr-TM (TM = Co, Ni) ternary alloys caused the formation of a coexistent Al + quasi-crystalline (Q) structure where the Q phase is included as a main constituent phase. Subsequently, a bulk alloy consisting of Q and Al was produced by extrusion of the atomized powder. The particle size and inter-particle spacing of the Q particles are 150 and 140 nm, respectively and the volume fraction is about 60%. The mixed phase alloy exhibit high tensile strength and elongation of 720 MPa and 6.4%, respectively for Al 93Mn 5Co 2 alloy. The Young's modulus is also as high as 92 GPa. The Al-based alloy exhibits a small coefficient of thermal expansion of 20 × 10 −6 K −1 between 373–473 K which is about 20% smaller than those for conventional Al alloys. These superior mechanical properties are presumably due to the fine dispersion and high volume fraction of Q particles and the high rigidness of the Q phase.

Improvement of Mechanical Properties by Precipitation of Nanoscale Compound Particles in Zr–Cu–Pd–Al Amorphous Alloys

The replacement of Cu by 10 at%Pd for an amorphous Zr 60 Cu 30 Al 10 alloy was found to change the crystallization process from the single stage of amorphous (Am)→Zr 2 Cu+Zr 2 Al to the two stages of Am→Am'+Zr 2 (Cu, Pd) →Zr 2 (Cu, Pd)+Zr 3 (Al, Pd) 2 in the maintenance of the wide supercooled liquid region before crystallization. After the melt-spun amorphous alloys were annealed for 1.2 ks at 726 K and the volume fraction (V f ) of compound reached as large as 75%, the particle size and interparticle spacing of the compound particles in the amorphous matrix were 10 and 1.5 nm, respectively. The residual amorphous phase enabled the maintenance of the nanoscale compound particles. The nanoscale mixed phase alloy remains good bending ductility even at V f =75% and exhibits high tensile strength (σ f ) of 1910 MPa which is higher than that (1640 MPa) for the amorphous single phase. The increase of the thermal stability of the remaining amorphous phase is presumably due to the generation of the strong bonding pair mainly among Zr, Pd and Al. The good ductility of the mixed phase alloy is due to the suppression of embrittlement for the remaining amorphous phase because the partial crystallization is made in the supercooled liquid region. The first achievement of high σ f and good ductility for the mixed phase alloy with nanoscale Zr 2 (Cu, Pd) phase surrounded by the amorphous phase is important for future progress of high-strength nanocrystalline bulk alloys.

High Strength Al–Ti–Fe Alloys Consisting of Amorphous and fcc-Al Phases Prepared by Rapid Solidification

Coexistent of amorphous and fcc-Al phases were formed in rapidly solidified Al 98-x Ti x Fe 2 (x=3, 5 and 8 at%) alloys. The structure consists of equiaxed Al grains embedded in the network of an amorphous phase. The grain size of the Al phase is 20 to 30 run and the interparticle spacing is about 7 nm for the Al 93 Ti 5 Fe 2 alloy. The volume fraction of the Al phase is evaluated to be 70 to 80%. The mixed structure is presumably formed through the solidification process of liquid primary fcc-Al+remaining liquid→Al+amorphous phases. The further increase in Ti content to 10 at% causes the formation of an amorphous single phase. The crystallization temperature (T x ) of the amorphous phase increases from 641 to 701 K with increasing Ti content from 3 to 10%. It is to be noticed that the T x values are much higher than that (⇇573 K) for AI-TM-Ln (TM=transition metal, Ln = lanthanide metal) amorphous alloys because of the low diffusivity of Ti. The mixed phase alloys have good bending ductility and exhibit the highest tensile strength (σ i ) of 1200 MPa for Al 93 Ti 5 Fe 2 . The ductility decreases with further increasing Ti content because of the transition from ductile to brittle nature for the amorphous phase and no high tensile strength exceeding 500 MPa is obtained for the amorphous single phase alloy. The formation of the finely mixed amorphous and Al phases with high σ f and T x values is important for the future development of Al-rich Al-Ti based alloys with high specific strength.

Formation of new metastable bcc phases by crystallization of amorphous Al 92La 8 and Al 92Ce 8 alloys

In the crystallization process of Al 92La 8 and Al 92Ce 8 amorphous alloys, new metastable phases were found to form as a primary crystalline phase. The Al 92La 8 and Al 92Ce 8 alloys were rapidly solidified into amorphous ribbons with a thickness of about 25 μm by a single roller method. As annealing temperature increases, the rapidly solidified Al 92La 8 amorphous alloy first changes into a metastable body-centered cubic (bcc) phase with a lattice parameter of a=0.6653 nm at 473 K, and then decomposes into α-Al and orthorhombic Al 11La 3 phases at 550 K. When the amorphous Al 92Ce 8 alloy is annealed at 473 K, the amorphous phase also changes into a metastable bcc phase with a lattice parameter of a= 1.3871 nm. With increasing temperature to 565 K, the metastable phase decomposes into α-Al and orthorhombic Al 11Ce 3 phases. The metastable bcc phases have high Vickers hardness numbers (≈ 300) which are about twice as high as those (≈ 168) for the amorphous single phase. The new metastable phases seem to be important for subsequent understanding of the amorphous structure for these alloys and the high strength of the crystallized mixed phase alloys.

Microstructure and mechanical properties of bulk Mg 70Ca 10Al 20 alloys produced by extrusion of atomized amorphous powders

The application of high-pressure Ar atomization to Mg 70Ca 10Al 20 alloy causes the formation of amorphous and Mg phases, and subsequent extrusion of the atomized powder at 673 K results in the formation of a bulky alloy with a finely mixed structure consisting of Al 2Ca embedded in an Mg matrix. The mixed phase alloy exhibits a high yield strength of 600 MPa, a high specific yield strength of 3.3 MNm kg −1, a high Young's modulus of 49 GPa at room temperature, a high elevated-temperature strength above 300 MPa in the range up to 550 K, and good corrosion resistance; these properties are superior to those of commercial Mg-based alloys. The simultaneous achievement of high mechanical strength and good corrosion resistance is attractive for subsequent development as a new type of high-strength materials.

特集 アルミニウム粉末冶金合金 急速凝固アルミニウム合金開発の現状と将来

This paper aims to review our recent results on the microstructure and mechanical properties of rapidly solidified Al-based alloys. The formation of non-periodic structures such as amorphous or icosahedral (I) phase by rapid solidification was found to cause the achievement of high tensile strength ( σf ) exceeding 1200 MPa combined with good bending ductility. The highest σf was 1260 MPa in an amorphous phase, 1560 MPa in coexistent amorphous and nanoscale Al phases and 1340 MPa in coexistent I and Al phases. The extrusion of atomized powders having the amorphous or I+A1 structure at appropriate temperatures caused the formation of bulky alloys with finely mixed structures consisting of Al+compound or Al+I+compound, respectively. The former mixed phase alloys exhibit high σf of 800 to 1000 MPa and elongation ( ep) of 1 to 7%, while the latter mixed phase alloys have high σf of 500 to 600 MPa combined with large ep of 15 to 25 %. These good mechanical properties allow us to expect that new type of high-strength and high-ductility alloys are produced as practical materials by utilizing the feature of the non-periodic structure.

Ultrahigh Strength of Rapidly Solidified Al<SUB>96−<I>x</I></SUB>Cr<SUB>3</SUB>Ce<SUB>1</SUB>Co<I><SUB>x</SUB></I> (<I>x</I>=1, 1.5 and 2%) Alloys Containing an Icosahedral Phase as a Main Component

An extremely high tensile strength (σf) of 1340 MPa combined with good bending ductility was obtained as a mixed structure consisting of nanoscale icosahedral (I) particles with a size of about 40 nm surrounded by a thin fcc-Al layer with a thickness of about 2 nm in rapidly solidified Al99−x−yCrxCe1Coy alloys containing 0 to 5%Cr and 0 to 1.5%Co. Furthermore, each I-particle has a random orientation and contains a high density of phason defects and subnanoscale approximant crystalline regions. The replacement of Co by Mn, Fe, Ni or Cu causes the decrease in σf through the increases in the particle size of the I-phase and the width of the Al phase as well as the decrease in the density of phason defects in the I-phase. The unique mixed structure is formed through the process of the precipitation of the primary I-phase, followed by the solidification of the remaining liquid as an Al phase. The good ductility for the alloys containing the I-phase as a main constitute is presumably due to the ease of the sliding along the interface between I- and approximant crystalline phases as well as the existence of the Al phase which surrounds the I-phase. The high σf value is interpreted by the effective contribution of the I-particles as a strengthening phase because of the achievement of a good ductile nature for the mixed phase alloys.

Effect of Cu or Ag on the Formation of Coexistent Nanoscale Al Particles in Al–Ni–M–Ce (M=Cu or Ag) Amorphous Alloys

The precipitation of a primary Al phase upon annealing of amorphous Al87Ni10Ce3, Al87Ni7Cu3Ce3 and Al87Ni8Ag2Ce3 alloys was found to occur only through a growth mechanism, based on the result that the exothermic reaction due to the precipitation of Al phase on the DSC curve does not have an incubation stage. The activation energy for the growth of the Al phase decreases from 1.82 eV for the Al–Ni–Ce alloy to 1.44 to 1.56 eV for the Al–Ni–M–Ce (M=Cu or Ag) alloys and the annealing temperature and time regions where the Al phase grows extend by the replacement of M for Ni. The particle size of the Al phase decreases from 9 nm for the ternary alloy to 3 to 5 nm for the quaternary alloys, accompanying the significant increase in the number of the Al particles. The extremely fine mixed structure consisting of nanoscale Al particles embedded in the amorphous matrix is formed in the Al–Ni–M–Ce alloys containing Cu or Ag elements which are soluble to the Al phase. The formation of the mixed structure is presumably due to the combination of (1) the necessity of the redistribution of the M elements for the growth of the Al particles resulting from the difference between the soluble content of the M elements into the Al particles and the nominal M content in the amorphous matrix, and (2) the increase in the number of the pre-existing nuclei of Al-rich zone resulting from the increase in the apparent Al content caused by the replacement of Ni by the M elements. The finding of the M elements leading to the refinement of the nanoscale Al particles is important in the subsequent development of the nanoscale mixed phase alloys.

Mg-based amorphous alloys

Recent progress in Mg-based amorphous alloys has been reviewed in the framework of the results obtained by the present authors. The amorphous alloys are formed in wide composition ranges in a number of Mg-based alloy systems by melt spinning. The amorphous alloys in MgLnTM (Ln ≡ lanthanide metal, TM ≡ transition metal) system exhibit a wide supercooled liquid region before crystallization and have large glass-forming ability which enables the production of bulk amorphous alloys with thickness below 7 mm by the high pressure die casting process. The bulk amorphous alloys were also found to exhibit high tensile strength above 600 MPa. Furthermore, by using the newly developed high pressure argon atomization equipment in which oxygen and moisture contents can be controlled to be below 1 ppm, Mg-based amorphous powders were produced in various alloy systems. The consolidation of the Mg-based amorpous powders resulted in finely mixed structures of Mg and compounds. The mixed phase alloys exhibit high tensile strengths at room and elevated temperatures for MgCuY and MgCaAl alloys and high corrosion resistance for MgCaAl alloys. The large glass-forming ability and these excellent properties for the Mg-based amorphous alloys are very attractive in applications for the subsequent development of the new alloys.

New Amorphous Al–Ni–Fe and Al–Ni–Co Alloys

New amorphous alloys were found to form by melt spinning in Al–Ni–Fe and Al–Ni–Co systems without lanthanide (Ln), Zr and Nb, which are known to be glass-forming elements for Al–based alloys. Coexistent amorphous and Al phases, and the amorphous phase also formed in the ranges of 0 to 14 at% Ni and 0 to 10%Fe or 0 to 14%Co. The mixed phase alloys containing more than 87%Al as well as the amorphous single phase alloys have good bending ductility. Tensile fracture strength (σf) and Vickers hardness (Hv) for the amorphous single phase are in the range 870 to 1070 MPa and 280 to 320, respectively. With decreasing cooling rate, the structure changes to Al and amorphous phases. σf and Hv increase to 1270 MPa and 360 without losing ductility in the mixed state where the volume fraction of the Al phase is about 20% and the particle size and interparticle spacing are about 10 nm and 30 nm, respectively. From the similarity in the mixed structure between the present alloys and the previously reported Al–Ni–Ln alloys, it is presumed that the increase in σf for the mixed phase alloys is due to the increase in strength of the Al particles resulting from the absence of internal defects as well as to the effective barrier of the Al particles against shear deformation of the amorphous matrix.

Cu-Rich Cu–Al–Ln (Ln=Ce or Nd) Amorphous Alloys

Cu-based amorphous alloys were found to form in Cu-Al-Ce and Cu-Al-Nd systems by rapid solidification. The composition ranges extend from 5 to 13 at%Al and 7 to 10%Ce or Nd for the amorphous single phase and 2 to 13%Al and 3 to 10%Ce or Nd for the amorphous plus fcc-Cu phases. The Cu-based alloys consisting of an amorphous single phase or amorphous plus fcc phases have good bending ductility and the tensile fracture strength is 990 to 1010 MPa for the amorphous alloys and increases to 1 190 to 1210 MPa for the mixed phase alloys. Electrical resistivity at room temperature is in the range of 660 to 790 nΩ.m for the amorphous phase and decreases to 350 to 590 nΩ.m for the mixed structure