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Journal articles on the topic 'Bulk alloys'

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Published: 10 December 2022
Last updated: 28 January 2023

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1

Chin, T. S., C. Y. Lin, M. C. Lee, R. T. Huang, and S. M. Huang. "Bulk nano-crystalline alloys." Materials Today 12, no. 1-2 (January 2009): 34–39. http://dx.doi.org/10.1016/s1369-7021(09)70044-6.

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2

Inoue, Akihisa, Akihiro Makino, and Takao Mizushima. "Ferromagnetic bulk glassy alloys." Journal of Magnetism and Magnetic Materials 215-216 (June 2000): 246–52. http://dx.doi.org/10.1016/s0304-8853(00)00127-x.

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3

Inoue, Akihisa, Akira Takeuchi, and Tao Zhang. "Ferromagnetic bulk amorphous alloys." Metallurgical and Materials Transactions A 29, no. 7 (July 1998): 1779–93. http://dx.doi.org/10.1007/s11661-998-0001-9.

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4

Eckert, J., A. Reger-Leonhard, B. Weiß, M. Heilmaier, and L. Schultz. "Bulk Nanostructured Multicomponent Alloys." Advanced Engineering Materials 3, no. 1-2 (January 2001): 41–47. http://dx.doi.org/10.1002/1527-2648(200101)3:1/2<41::aid-adem41>3.0.co;2-s.

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5

Takeuchi, A., N. Chen, T. Wada, W. Zhang, Y. Yokoyama, A. Inoue, and J. W. Yeh. "Alloy Design for High-Entropy Bulk Glassy Alloys." Procedia Engineering 36 (2012): 226–34. http://dx.doi.org/10.1016/j.proeng.2012.03.035.

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6

Cao, Peng Jun, Ji Ling Dong, and Hai Dong Wu. "Research on Cu-Based Bulk Glassy Alloys and its Mechanical Properties." Applied Mechanics and Materials 329 (June 2013): 127–32. http://dx.doi.org/10.4028/www.scientific.net/amm.329.127.

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High-strength Cu-based bulk glassy alloys with a large supercooled liquid region in Cu-Zr-Ti-Ni systems were prepared by means of copper mold casting. The Cu-based bulk glassy alloys samples were tested by X-ray diffraction (XRD), differential scanning calorimetry (DSC), scanning electron microscopy (SEM) and Instron testing machine. The result indicates, the maximum diameter was 5.0 mm for the Cu55Zr25Ti15Ni5 bulk glassy alloy. The temperature interval of supercooled liquid region (ΔTx) is as large as 45.48-70.98 K for the Cu-Zr-Ti-Ni alloy. The Cu-based glassy alloys rods exhibited the very high mechanical properties and the distinct plastic strains. The compressive fracture strength is 2155 MPa, 2026 MPa and 1904 MPa respectively for Cu50Zr25Ti15Ni10, Cu55Zr25Ti15Ni5 and Cu54Zr22Ti18Ni6 bulk glassy alloys. The Vickers hardness is respectively 674, 678 and 685 for the Cu50Zr25Ti15Ni10, Cu55Zr25Ti15Ni5 and Cu54Zr22Ti18Ni6 bulk glassy alloys. The addition Co element to Cu-Zr-Ti-Ni alloy expand the ΔTx, the ΔTx is 74.5 K for Cu50Zr22Ti18Ni6Co4 bulk glassy alloys.
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7

Inoue, A., B. L. Shen, A. R. Yavari, and A. L. Greer. "Mechanical properties of Fe-based bulk glassy alloys in Fe–B–Si–Nb and Fe–Ga–P–C–B–Si systems." Journal of Materials Research 18, no. 6 (June 2003): 1487–92. http://dx.doi.org/10.1557/jmr.2003.0205.

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Mechanical properties of cast Fe-based bulk glassy alloy rods with compositions of (Fe0.75B0.15Si0.1)96Nb4 and Fe77Ga3P9.5C4B4Si2.5 were examined by compression and Vickers hardness tests. The Young's modulus (E), yield strength (σy), fracture strength (σf), elastic strain (εe), fracture strain (εf), and Vickers hardness (Hv) were 175 GPa, 3165 MPa, 3250 MPa, 1.8%, 2.2%, and 1060, respectively, for the former alloy and 182 GPa, 2980 MPa, 3160 MPa, 1.9%, 2.2%, and 870, respectively, for the latter alloy. The εf /E and Hv/3E were 0.019–0.017 and 0.020–0.016, respectively, for the alloys, in agreement with the previous data for a number of bulk glassy alloys. The agreement suggests that these Fe-based bulk glassy alloys have an elastic–plastic deformation mode. The syntheses of high-strength Fe-based bulk glassy alloys with distinct compressive plastic strain and elastic–plastic deformation mode are encouraging for future development of Fe-based bulk glassy alloys as structural and soft magnetic materials.
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8

Inoue, Akihisa. "Slowly-Cooled Bulk Amorphous Alloys." Materials Science Forum 179-181 (February 1995): 691–700. http://dx.doi.org/10.4028/www.scientific.net/msf.179-181.691.

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9

YOKOYAMA, Yoshihiko, and Akihisa INOUE. "Cast of Bulk Glassy Alloys." Journal of the Society of Materials Science, Japan 58, no. 3 (2009): 193–98. http://dx.doi.org/10.2472/jsms.58.193.

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10

Xing, L. Q., P. Ochin, M. Harmelin, F. Faudot, J. Bigot, and J. P. Chevalier. "Cast bulk ZrTiAlCuNi amorphous alloys." Materials Science and Engineering: A 220, no. 1-2 (December 1996): 155–61. http://dx.doi.org/10.1016/s0921-5093(96)10454-8.

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11

Pryds, N. H. "Bulk amorphous Mg-based alloys." Materials Science and Engineering: A 375-377 (July 2004): 186–93. http://dx.doi.org/10.1016/j.msea.2003.10.147.

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12

Tully, Katherine, and John Monaghan. "Bulk forming of superplastic alloys." Journal of Materials Processing Technology 26, no. 2 (June 1991): 159–71. http://dx.doi.org/10.1016/0924-0136(91)90130-7.

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13

Inoue, A., T. Zhang, and A. Takeuchi. "Hard magnetic bulk amorphous alloys." IEEE Transactions on Magnetics 33, no. 5 (1997): 3814–16. http://dx.doi.org/10.1109/20.619580.

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14

Grammatikakis, J., M. Manolopoulos, V. Katsika, and D. Kostopoulos. "Bulk moduli of F.C.C. alloys." Physica Status Solidi (a) 144, no. 2 (August 16, 1994): 317–27. http://dx.doi.org/10.1002/pssa.2211440210.

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15

Li, Li Xin. "Properties of Ni-Cu Bulk Alloy Prepared by Spark Plasma Sintering Technique." Advanced Materials Research 476-478 (February 2012): 949–53. http://dx.doi.org/10.4028/www.scientific.net/amr.476-478.949.

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Ni-Cu bulk alloys were successfully prepared with spark plasma sintering (SPS) technique from nanopowders obtained by the arc plasma evaporation method. The tensile tests indicated that the tensile strength of Ni-Cu bulk alloy sintered by SPS at 600°C was the highest among the Ni-Cu bulk alloys sintered at different temperature and much higher than that of bulk ingots. Through investigating the fractographs of the bulk alloy, the intrinsic reasons for the tensile strength of the sintered specimens were discussed.
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16

Na, J. H., E. S. Park, Y. C. Kim, E. Fleury, W. T. Kim, and D. H. Kim. "Poisson’s ratio and fragility of bulk metallic glasses." Journal of Materials Research 23, no. 2 (February 2008): 523–28. http://dx.doi.org/10.1557/jmr.2008.0060.

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The correlation among apparent global plasticity, Poisson’s ratio, and fragility in monolithic bulk metallic glass (BMG) alloys has been investigated in the present study. The shear and bulk moduli in monolithic Cu-based BMG alloys have been measured by resonant ultrasound spectroscopy (RUS) and ultrasonic technique. The Cu43Zr43Al7Ag7 BMG alloy showing a large apparent global plasticity (∼8%) exhibits a high Poisson’s ratio when compared with that of Cu43Zr43Al7Be7 BMG alloy. In addition, the fragility of Cu-based BMG alloys can be obtained by differential scanning calorimetry (DSC). The fragility index m of Cu43Zr43Al7Ag7 BMG alloy is slightly larger than that of Cu43Zr43Al7Be7 BMG alloy. The correlation between Poisson’s ratio and fragility in BMG alloys can be presented by a simple relation of m − 17 = 14 (B∞/G∞ − 1). Poisson’s ratio and fragility might be regarded as an important parameter that controls global plasticity of glass-forming alloys.
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17

Cao, Peng Jun, Ji Ling Dong, Hai Dong Wu, and Pei Geng Fan. "Preparation and Corrosion Resistance of Cu-Based Bulk Glassy Alloys." Advanced Materials Research 652-654 (January 2013): 1143–48. http://dx.doi.org/10.4028/www.scientific.net/amr.652-654.1143.

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The Cu-based bulk glassy alloys in Cu-Zr-Ti-Ni systems were prepared by means of copper mold casting. The structure and corrosion resistance of Cu-based bulk glassy alloys were analyzed by X-ray diffraction (XRD), differential scanning calorimetry (DSC), electrochemistry method, lost weight method. The result indicates the supercooled liquid temperature interval (ΔTx) is up to 70.98 K for Cu50Zr25Ti15Ni10bulk glassy alloy. The maximum diameter was up to 5.0 mm for the Cu55Zr25Ti15Ni5bulk glassy alloy. For electrochemistry corrosion in 3.5% NaCl solution, self-corrosion electric current density of the Cu50Zr25Ti15Ni10bulk glassy alloys is obviously lower than that of stainless steel and brass, so corrosion resistance of Cu-based bulk glassy alloys is better than stainless steel and brass at the same corrosion condition. The lost weight method showed that the corrosion rate of brass, stainless steel and glassy alloy is respectively 10.08 g/(m2•h), 6.08 g/(m2•h) and 2.19 g/(m2•h) in the 3% NaCl solution, which also indicates that the corrosion resistance of Cu-based bulk glassy alloys is better than stainless steel and brass. The Cu-based bulk glassy alloys can be used in the special field demanding to have the super high strength, hardness and corrosion resistance.
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18

Takeuchi, Akira. "Alloy Designs for High-Entropy Alloys, Bulk Metallic Glasses and High-Entropy Bulk Metallic Glasses." Journal of the Japan Institute of Metals 79, no. 4 (2015): 157–68. http://dx.doi.org/10.2320/jinstmet.j2014046.

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19

Yi, S., T. G. Park, and D. H. Kim. "Ni-based bulk amorphous alloys in the Ni–Ti–Zr–(Si, Sn) system." Journal of Materials Research 15, no. 11 (November 2000): 2425–30. http://dx.doi.org/10.1557/jmr.2000.0348.

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New Ni-based bulk amorphous alloys in the alloy system Ni–Ti–Zr–(Si,Sn) were developed through systematic alloy design based upon the empirical rules for high glass forming alloys. Small additions of Si and/or Sn significantly improved the glass forming ability (GFA) of the alloys Ni57Ti23−xZr20 (Si,Sn)x leading to a Ni-based bulk amorphous alloy. The amorphous ribbons of the alloys Ni57Ti23−xZr20 (Si,Sn)x exhibited very high glass transition temperatures (Tg > 823 K), crystallization temperatures (Tx > 883 K), and large undercooled liquid regions (δTx > 50 K) implying the high GFA of the alloys. Fully amorphous rods with the diameter of up to 2 mm can be fabricated by a copper mold casting method. Development of the new Ni-based bulk amorphous alloys having high Tg,Tx, and δTx expands the practical applications of amorphous alloys as structural materials.
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20

Wu, Fang, Qinglin He, Mingsheng Tang, and Hongzhang Song. "Thermoelectric properties of Tl and I dual-doped Bi2Te3-based alloys." International Journal of Modern Physics B 32, no. 10 (April 13, 2018): 1850123. http://dx.doi.org/10.1142/s0217979218501230.

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Tl[Formula: see text]Bi[Formula: see text]Te[Formula: see text]I[Formula: see text] (x = 0, 0.05, 0.1 and 0.2) flower-like nanopowders were prepared successfully by the hydrothermal method. Then, the synthesized nanoparticles were pressed into bulks by hot-pressing. The thermoelectric (TE) properties of the Tl[Formula: see text]Bi[Formula: see text]Te[Formula: see text]I[Formula: see text] bulk samples were investigated and discussed. The results showed that the influences of Tl doping on the electrical resistivity and Seebeck coefficients of the Bi2Te3 is over that of I doping. Thus, the power factors of the dual-doped bulks are all less than that of the Bi2Te3 bulk. The thermal conductivities of the Tl[Formula: see text]Bi[Formula: see text]Te[Formula: see text]I[Formula: see text] bulk samples also remain at lower values. As a result, the ZT value of the optimized doped bulk Tl[Formula: see text]Bi[Formula: see text]Te[Formula: see text]I[Formula: see text] attains a value of 1.1 at 398 K.
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21

Hashimoto, Koji, H. Katagiri, H. Habazaki, M. Yamasaki, A. Kawashima, K. Izumiya, H. Ukai, Katsuhiko Asami, and S. Meguro. "Extremely Corrosion-Resistant Bulk Amorphous Alloys." Journal of Metastable and Nanocrystalline Materials 11 (June 2001): 1–8. http://dx.doi.org/10.4028/www.scientific.net/jmnm.11.1.

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22

Hashimoto, Koji, H. Katagiri, H. Habazaki, M. Yamasaki, A. Kawashima, K. Izumiya, H. Ukai, Katsuhiko Asami, and S. Meguro. "Extremely Corrosion-Resistant Bulk Amorphous Alloys." Materials Science Forum 377 (June 2001): 1–8. http://dx.doi.org/10.4028/www.scientific.net/msf.377.1.

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23

卢, 静. "Research Advances in Bulk Amorphous Alloys." Material Sciences 06, no. 04 (2016): 245–50. http://dx.doi.org/10.12677/ms.2016.64031.

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24

Fan, Cang, P. K. Liaw, T. W. Wilson, W. Dmowski, H. Choo, C. T. Liu, J. W. Richardson, and Th Proffen. "Structural model for bulk amorphous alloys." Applied Physics Letters 89, no. 11 (September 11, 2006): 111905. http://dx.doi.org/10.1063/1.2345276.

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25

Chan, F. W., N. G. Ma, and H. W. Kui. "Compaction of bulk ferromagnetic Fe80P13C7amorphous alloys." Journal of Materials Research 16, no. 10 (October 2001): 2767–69. http://dx.doi.org/10.1557/jmr.2001.0377.

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When bulk ferromagnetic Fe80P13C7 amorphous rods of approximately 2-mm diameter are compacted together in a hot press, a variety of different microstructures, depending on the experimental conditions, are produced. The most intriguing microstructure is that two different bulk amorphous rods can be fused together perfectly at a temperature of 683 K and under a pressure of 2.5 to 4 GPa for a period of 5 min.
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26

Li, Qiang. "Compaction of bulk amorphous Fe40Ni40P14B6 alloys." Materials Science and Engineering: A 471, no. 1-2 (December 2007): 75–81. http://dx.doi.org/10.1016/j.msea.2007.02.118.

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27

Lee, Seok-Woo, Sang-Chul Lee, and Jae-Chul Lee. "Plasticity criterion for bulk amorphous alloys." Materials Science and Engineering: A 477, no. 1-2 (March 2008): 344–49. http://dx.doi.org/10.1016/j.msea.2007.05.036.

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28

Inoue, Akihisa, T. Zhang, and Akira Takeuchi. "Ferrous and Nonferrous Bulk Amorphous Alloys." Materials Science Forum 269-272 (January 1998): 855–64. http://dx.doi.org/10.4028/www.scientific.net/msf.269-272.855.

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29

Inoue, Akihisa, and Akira Takeuchi. "Recent Progress in Bulk Glassy Alloys." MATERIALS TRANSACTIONS 43, no. 8 (2002): 1892–906. http://dx.doi.org/10.2320/matertrans.43.1892.

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30

Yuan, Guangyin, Cunling Qin, and Akihisa Inoue. "Mg-based bulk glassy alloys with high strength above 900 MPa and plastic strain." Journal of Materials Research 20, no. 2 (February 2005): 394–400. http://dx.doi.org/10.1557/jmr.2005.0044.

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Bulk metallic glasses with a maximum diameter of 2.5–5 mm were formed in Mg75Cu5Ni10Gd10, Mg70Cu15Ni5Gd10, and Mg65Cu20Ni5Gd10 systems by copper mold casting. There is a clear tendency for glass-forming ability (GFA) to increase with increasing solute content. These bulk glassy alloys exhibit a large supercooled liquid region (ΔTx) of 44–64 K, indicating high thermal stability of the supercooled liquid. The Young’s modulus, fracture strength, elastic elongation limit, and plastic strain are in the range of 54–59 GPa, 854–904 MPa, 1.50–1.55%, and 0.10–0.20%, respectively. The Mg65Cu20Ni5Gd10 alloy exhibited the highest values of Young’s modulus and strength, while the largest plastic strain was obtained for the Mg75Cu5Ni10Gd10 alloy. The bulk Mg–Cu–Ni–Gd-based metallic glasses exhibited distinct enhanced corrosion resistance compared to Mg65Cu25Gd10 glassy alloy in NaCl aqueous solutions. The fabrication of the Mg-based bulk glassy alloys exhibiting a high strength level of about 900 MPa and plastic strains of ∼0.2%, in conjunction with good corrosion resistance, indicates that the Mg-based bulk glassy alloys may be used as a new generation of structural material.
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31

Zhang, Qing Sheng, Wei Zhang, Dmitri V. Louzguine-Luzgin, and Akihisa Inoue. "High Glass-Forming Ability and Unusual Deformation Behavior of New Zr-Cu-Fe-Al Bulk Metallic Glasses." Materials Science Forum 654-656 (June 2010): 1042–45. http://dx.doi.org/10.4028/www.scientific.net/msf.654-656.1042.

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A new series of bulk metallic glasses were developed by addition of Fe into the ternary Zr60Cu30Al10 alloy. Although Fe-Cu element pair shows distinct immiscibility with a large positive heat of mixing, substitution of Fe for Cu significantly improves the glass-forming ability of the ternary Zr60Cu30Al10 alloy. The critical diameter for glass-formation increases from 8 mm for Zr60Cu30Al10 alloy to 20 mm for Zr60Cu25Fe5Al10 and Zr62.5Cu22.5Fe5Al10 alloys. As compared with the ternary Zr60Cu30Al10 alloy, the new quaternary Zr-Cu-Fe-Al alloys show lower liquidus temperatures. The Zr60Cu25Fe5Al10 and Zr62.5Cu22.5Fe5Al10 alloys, the best BMG-formers in this alloy system, are found to locate very near a Zr-Cu-Fe-Al eutectic point. The new Zr-Fe-Cu-Al bulk metallic glasses exhibit high strength of about 1700 MPa. The plastic strain increases from 7.8% to 11.3% with increasing the content of Fe from 0 to 12.5%. The finding of a Ni-free Zr-based bulk glassy alloy with the extremely high glass-forming ability is expected to extend the future application of bulk metallic glasses.
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32

Louzguine-Luzgin, Dmitri V., Takanobu Saito, Junji Saida, and Akihisa Inoue. "Thermal conductivity of metallic glassy alloys and its relationship to the glass forming ability and the observed cooling rates." Journal of Materials Research 23, no. 8 (August 2008): 2283–87. http://dx.doi.org/10.1557/jmr.2008.0286.

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In this work, we study the cooling behavior of several typical bulk glassy alloys on casing and present the relationship between the thermal conductivity of a glassy alloy and the cooling rate upon mold casting. The cooling rates obtained for Ti-, Zr-, Pd-, and Cu-based bulk glass forming alloys are found to scale with the thermal conductivities of the studied glassy alloys.
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33

Asami, Katsuhiko, H. Habazaki, Akihisa Inoue, and Koji Hashimoto. "Recent Development of Highly Corrosion Resistant Bulk Glassy Alloys." Materials Science Forum 502 (December 2005): 225–30. http://dx.doi.org/10.4028/www.scientific.net/msf.502.225.

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Recent development of corrosion resistant bulk glassy alloys such as Zr-, Fe-, Ni- and Cu-base alloys were presented. It was clarified that the enrichment of cations in the passive film, which is responsible to corrosion resistance, depends on both alloy composition and environment. TEM observation also made it clear that alloys lose their advantageous properties such as corrosion resistance when they are devoid of or lose amorphous structure even in part due to low glass forming ability or heating. These findings were essentially similar to those of conventional amorphous alloys.
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34

Jeż, Bartłomiej, Jerzy Wysłocki, Simon Walters, Przemysław Postawa, and Marcin Nabiałek. "The Process of Magnetizing FeNbYHfB Bulk Amorphous Alloys in Strong Magnetic Fields." Materials 13, no. 6 (March 18, 2020): 1367. http://dx.doi.org/10.3390/ma13061367.

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The structure of amorphous alloys still has not been described satisfactorily due to the lack of direct methods for observing structural defects. The magnetizing process of amorphous alloys is closely related to its disordered structure. The sensitivity of the magnetization vector to any heterogeneity allows indirect assessment of the structure of amorphous ferromagnetic alloys. In strong magnetic fields, the magnetization process involves the rotation of a magnetization vector around point and line defects. Based on analysis of primary magnetization curves, it is possible to identify the type of these defects. This paper presents the results of research into the magnetization process of amorphous alloys that are based on iron, in the areas called the approach to ferromagnetic saturation and the Holstein–Primakoff para-process. The structure of a range of specially produced materials was examined using X-ray diffraction. Primary magnetization curves were measured over the range of 0 to 2 T. The process of magnetizing all of the tested alloys was associated with the presence of linear defects, satisfying the relationship Ddi p < 1H. It was found that the addition of yttrium, at the expense of hafnium, impedes the magnetization process. The alloy with an atomic content of Y = 10% was characterized by the highest saturation magnetization value and the lowest value of the Dspf parameter, which may indicate the occurrence of antiferromagnetic ordering in certain regions of this alloy sample.
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35

Chin, T. S., C. Y. Lin, M. C. Lee, R. T. Huang, and S. M. Huang. "Bulk nano-crystalline Fe-based alloys by annealing bulk glassy precursors." Intermetallics 16, no. 1 (January 2008): 52–57. http://dx.doi.org/10.1016/j.intermet.2007.07.015.

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36

Baricco, Marcello, Tanya A. Başer, Gianluca Fiore, Rafael Piccin, Marta Satta, Alberto Castellero, Paola Rizzi, and Livio Battezzati. "Bulk Metallic Glasses." Materials Science Forum 604-605 (October 2008): 229–38. http://dx.doi.org/10.4028/www.scientific.net/msf.604-605.229.

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Rapid quenching techniques have been successfully applied since long time for the preparation of metallic glasses in ribbon form. Only in the recent years, the research activity addressed towards the synthesis of bulk metallic glasses (BMG), in form of ingots with a few millimetres in thickness. These materials can be obtained by casting techniques only for selected alloy compositions, characterised by a particularly high glass-forming tendency. Bulk amorphous alloys are characterised by a low modulus of elasticity and high yielding stress. The usual idea is that amorphous alloys undergo work softening and that deformation is concentrated in shear bands, which might be subjected to geometrical constraints, resulting in a substantial increase in hardness and wear resistance. The mechanical properties can be further improved by crystallisation. In fact, shear bands movement can be contrasted by incorporating a second phase in the material, which may be produced directly by controlled crystallisation. Soft magnetic properties have been obtained in Fe-based systems and they are strongly related to small variations in the microstructure, ranging from a fully amorphous phase to nanocrystalline phases with different crystal size. The high thermal stability of bulk metallic glasses makes possible the compression and shaping processes in the temperature range between glass transition and crystallisation. Aim of this paper is to present recent results on glass formation and properties of bulk metallic glasses with various compositions. Examples will be reported on Zr, Fe, Mg and Pd-based materials, focussing on mechanical and magnetic properties.
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37

Wang, Xin Lu, Wan Qiang Liu, Shan Shan Zhang, and Li Min Wang. "Preparation and Mechanical Properties of a Bulk Icosahedral Quasicrystalline Ti-Zr-Sc-Ni Alloy." Advanced Materials Research 415-417 (December 2011): 1153–56. http://dx.doi.org/10.4028/www.scientific.net/amr.415-417.1153.

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The discovery of the icosahedral quasicrystalline phase (i-phase) in as-cast Ti40.83Zr40.83-xScxNi18.34(x = 0~2.0) alloys is described herein. The effect of Sc on the structure and mechanical properties of the bulk quasicrystalline alloys is investigated. The results show that the phase structure of the as-cast alloys are mainly composed of icosahedral phase accompanied by minor C14 Laves phase (L-phase), and the mechanical properties of the bulk quasicrystalline alloys have been examined at room temperature, the compressive fracture strength first increased and then decreased with increasing x from 0.4 to 2.0, and the highest strength is near 1400 MPa when x =1.2, it was 380 MPa higher than the without Sc alloy. The bulk quasicrystalline alloy exhibits the elastic deformation by the compressive test, and the fracture mode was brittle cleavage fracture.
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38

BASKOUTAS, S., V. KAPAKLIS, and C. POLITIS. "BULK AMORPHOUS Zr57Cu20Al10Ni8Ti5 AND Zr55Cu19Al8Ni8Ti5Si5 ALLOYS PREPARED BY ARC MELTING." International Journal of Modern Physics B 16, no. 24 (September 20, 2002): 3707–14. http://dx.doi.org/10.1142/s0217979202013018.

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We have produced bulk amorphous materials by quenching arc melted melts in water cooled copper die. Alloys of the composition Zr 57 Cu 20 Al 10 Ni 8 Ti 5 and Zr 55 Cu 19 Al 8 Ni 8 Ti 5 Si 5 were produced in the form of small cylinders with a diameter of 3 mm and a length of 25 mm. The alloys were investigated by X-ray diffraction and thermal analysis to determine the structure and thermal properties. Complete amorphous X-ray patterns were observed for both alloys. The glass transition temperature is 362°C for the Zr 57 Cu 20 Al 10 Ni 8 Ti 5 alloy and 363°C for the Zr 55 Cu 19 Al 8 Ni 8 Ti 5 Si 5 alloy. The crystallization temperature of the Zr 57 Cu 20 Al 10 Ni 8 Ti 5 alloy was measured to be 414.6°C. The Zr 55 Cu 19 Al 8 Ni 8 Ti 5 Si 5 alloy has a higher crystallization temperature of 425.5°C.
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39

Sun, Haoliang, Xiaoxue Huang, Xinxin Lian, and Guangxin Wang. "Discrepancies in the Microstructures of Annealed Cu–Zr Bulk Alloy and Cu–Zr Alloy Films." Materials 12, no. 15 (August 2, 2019): 2467. http://dx.doi.org/10.3390/ma12152467.

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Copper–zirconium bulk alloy and Cu–Zr alloy films are prepared by vacuum smelting and magnetron sputtering, respectively, and subsequently annealing is conducted. Results show that Cu–Zr bulk alloy and alloy films exhibit significantly different microstructure evolution behaviors after annealing due to different microstructures and residual stress states. CuxZr alloy compounds disperse at the grain boundary of Cu grains in as-cast and annealed Cu–Zr bulk alloys. However, unlike bulk alloys, a large number of polyhedral Cu particles are formed on the Cu–Zr thin films’ surface upon thermal annealing. Kinetically, the residual compressive stress in the Cu–Zr films promotes the formation of Cu particles. The influencing factors and the path for mass transport in the formation of the particles are discussed. The large-specific surface area particles/film composite structure has potential applications in Surface-Enhanced Raman Scattering, catalysis, and other fields.
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40

Takeuchi, Akira, Kenji Amiya, Takeshi Wada, Kunio Yubuta, Wei Zhang, and Akihiro Makino. "Entropies in Alloy Design for High-Entropy and Bulk Glassy Alloys." Entropy 15, no. 12 (September 12, 2013): 3810–21. http://dx.doi.org/10.3390/e15093810.

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41

BANERJEE, S., S. RAVY, J. DENLINGER, X. CHEN, D. K. SALDIN, and B. P. TONNER. "The STRUCTURE OF THE c(2×2) Mn/Ni(001) SURFACE ALLOY BY PHOTOELECTRON DIFFRACTION." Surface Review and Letters 04, no. 06 (December 1997): 1131–37. http://dx.doi.org/10.1142/s0218625x97001425.

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Surface alloys are two-dimensional metallic systems that can have structures that are unique to the surface, and have no counterpart in the bulk binary phase diagram. A very unusual structure was reported for the Mn–Ni system, based on a quantitative LEED structure determination, which showed that the Mn atoms were displaced out of the surface by a substantial amount. This displacement was attributed to a large magnetic moment on the Mn atoms. The structure of the Mn–Ni surface alloy was proposed to be based on a bulk termination model. Magnetic measurements on Mn–Ni, however, showed conclusively that the magnetic structure of these surface alloys is distinct from the bulk alloy analogs. For example, bulk MnNi is an antiferromagnet, whereas the surface alloy is ferromagnetic. This suggests that the proposed structure, based on bulk termination, is not complete. Photoelectron diffraction techniques were used to investigate this structure, using both a comparison to multiple scattering calculations and photoelectron holography.
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42

Li, Lin Bo, Jing Guo, and Fei Peng Lou. "Corrosion Behavior of Sm-Based Bulk Metallic Glasses in Salt Solution." Applied Mechanics and Materials 229-231 (November 2012): 26–30. http://dx.doi.org/10.4028/www.scientific.net/amm.229-231.26.

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In this paper, the corrosion behaviors of Sm-based bulk metallic glasses (BMGs) were investigated by immersion test. It was found that with Co content increasing the ability of corrosion resistance of the alloy increases for Sm-based bulk metallic glasses. A comparison study was made on the corrosion behaviors between the glassy state alloys and crystalline alloys with the same ingredients. The results show that the glassy state alloy has the better corrosion resistance.
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43

Bakulin, Alexander, Alexander Latyshev, and Svetlana Kulkova. "Absorption and Diffusion of Oxygen in Ti-Al Bulk Alloys." Solid State Phenomena 258 (December 2016): 408–11. http://dx.doi.org/10.4028/www.scientific.net/ssp.258.408.

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The oxygen absorption and diffusion properties are studied in γ-TiAl and TiAl3 alloys within density functional theory using projector augmented wave method in the plane-wave basis. It is shown that the octahedral site inside the Ti-rich octahedron is preferable for oxygen in case of γ-TiAl alloy whereas the Al-rich octahedron is more favorable environment for oxygen in TiAl3. It is shown that the energy barriers for oxygen jumps between different sites in bulk alloys depend significantly on the local environments of oxygen and increase for its jump from Ti-rich sites. The trajectories with minimum energy barriers are determined for both Ti-Al alloys. It is shown that the increase of Al content in alloy leads to the decrease of barriers for oxygen jumps.
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44

Shin, Seung Y., J. H. Kim, D. M. Lee, Jong K. Lee, H. J. Kim, Ha Guk Jeong, and Jung Chan Bae. "New Cu-Based Bulk Metallic Glasses with High Strength of 2000 MPa." Materials Science Forum 449-452 (March 2004): 945–48. http://dx.doi.org/10.4028/www.scientific.net/msf.449-452.945.

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New Cu-based bulk amorphous alloys exhibiting a large supercooled liquid region and good mechanical properties were formed in a quaternary Cu-Ni-Zr-Ti systems consisting of only metallic elements. The compositional range for the formation of the amorphous alloys that have high glass forming ability (GFA) (> 3 mm diameter) and large supercooled liquid region (> 50 K) is defined in the pseudo-ternary phase diagram Cu-Ni-(Zr, Ti). A bulk amorphous Cu54Ni6Zr22Ti18alloy with the diameter of 6 mm can be prepared by copper mold casting. The Cu54Ni6Zr22Ti18alloy shows glass transition temperature (Tg) of 712 K, crystallization temperature (Tx) of 769 K and supercooled liquid region (ΔTx) of 57 K. The Cu54Ni6Zr22Ti18alloy exhibits high compressive fracture strength of about 2130 MPa with a plastic strain of about 1.5 %. The new Cu-based bulk amorphous alloy with high GFA and good mechanical properties allows us to expect the extension of application fields as a new engineering material.
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45

Pang, Shujie, Tao Zhang, Katsuhiko Asami, and Akihisa Inoue. "Formation of Bulk Glassy Fe75–x–yCrxMoyC15B10 Alloys and Their Corrosion Behavior." Journal of Materials Research 17, no. 3 (March 2002): 701–4. http://dx.doi.org/10.1557/jmr.2002.0100.

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Formation of bulk Fe-based glassy alloys with high corrosion resistance was succeeded in the Fe75–x–yCrxMoyC15B10 alloy system. A large temperature interval of supercooled liquid region (ΔTx) of 40–90 K was obtained over a wide composition range for the Fe75?x–yCrxMoyC15B10 alloys. The Fe75–x–yCrxMoyC15B10 alloys were prepared in a bulk glassy form with diameters of 1.0–2.5 mm by copper mold casting. The bulk glassy Fe75–x–yCrxMoyC15B10 alloys exhibited high corrosion resistance in 1 N HCl solution. The glassy alloys containing Cr were spontaneously passivated with a wide passive region before the transpassive dissolution of Cr. The passive current density decreased significantly with an increase of alloying Cr content, indicating that the addition of Cr was effective on enhancing the corrosion resistance. Excess addition of Mo for replacing Fe in the present alloys was detrimental for the corrosion resistance.
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46

Akinlade, O., and A. O. Boyo. "Thermodynamics and surface properties of Fe–V and Fe–Ti liquid alloys." International Journal of Materials Research 95, no. 5 (May 1, 2004): 387–95. http://dx.doi.org/10.1515/ijmr-2004-0081.

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Abstract A simple statistical mechanical model, based on a quasi-lattice approximation in which one assumes the formation of complexes, has been used to study bulk properties, such as free energy of mixing, the thermodynamic activity and enthalpy of mixing, in liquid Fe –Vand Fe –Ti alloys. The energetics and its effect on the alloying behavior of the liquid alloys has been investigated with the aim of correlating bulk phenomena with surface effects. The analysis shows that, assuming the formation of intermetallic complexes of the form Fe2V and FeTi in the liquid alloys, one can explain the energetics of the bulk alloys. Our results for the bulk calculations indicate that Fe –V and Fe –Ti both exhibit a significant tendency for compound formation. From a perusal of the diffusion coefficient D, we observe the same trend towards compound formation, as demonstrated by the chemical short-range order parameter (CSRO) close to the assumed stoichiometric composition. Furthermore, using the model calculations in the bulk, we study some surface properties. Our calculations indicate that Fe segregates to the surface at all bulk compositions in Fe –Vand Fe –Ti liquid, though the segregation effect is more pronounced in the former alloy. The reason for this is that Fe –Ti is a more ordered system than Fe –V and, thus, the driving force for surface segregation in these alloys is their energetics.
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47

Johnson, William L. "Bulk Glass-Forming Metallic Alloys: Science and Technology." MRS Bulletin 24, no. 10 (October 1999): 42–56. http://dx.doi.org/10.1557/s0883769400053252.

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The following article is based on the MRS Medal talk presented by William L. Johnson at the 1998 MRS Fall Meeting on December 2, 1998. The MRS Medal is awarded for a specific outstanding recent discovery or advancement that has a major impact on the progress of a materials-related field. Johnson received the honor for his development of bulk metallic glass-forming alloys, the fundamental understanding of the thermodynamics and kinetics that control glass formation and crystallization of glass-forming liquids, and the application of these materials in engineering.The development of bulk glass-forming metallic alloys has led to interesting advances in the science of liquid metals. This article begins with brief remarks about the history and background of the field, then follows with a discussion of multicomponent glass-forming alloys and deep eutectics, the chemical constitution of these new alloys, and how they differ from metallic glasses of a decade ago or earlier. Recent studies of deeply undercooled liquid alloys and the insights made possible by their exceptional stability with respect to crystallization will then be discussed. Advances in this area will be illustrated by several examples. The article then describes some of the physical and specific mechanical properties of bulk metallic glasses (BMGs), and concludes with some interesting potential applications.The first liquid-metal alloy vitrified by cooling from the molten state to the glass transition was Au-Si, as reported by Duwez at Caltech in 1960. Duwez made this discovery as a result of developing rapid quenching techniques for chilling metallic liquids at very high rates of 105–106 K/s.
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Radu, Bogdan, Dragoş Buzdugan, Cosmin Codrean, Viorel Aurel Şerban, and George Vișan. "Numerical Model of Thermal Field Developed in Fe67Cr4Mo4Ga4P12B5C4 Bulk Amorphous Alloy Processing." Solid State Phenomena 254 (August 2016): 249–54. http://dx.doi.org/10.4028/www.scientific.net/ssp.254.249.

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Metallic amorphous materials were developed during 80’s as new materials, with very interesting industrial properties (heat conductivity, magnetic properties, fusion temperature, corrosion resistance, etc.). Technology to obtain these materials, based on very rapid cooling of a melted alloy with glass forming ability, has limitations for the dimensions of the products that can be obtained with amorphous structure (thickness has to be very thin), which can be overpassed by development of bulk amorphous alloys with high glass forming ability and good control of the cooling speed. Numerical modeling of thermal field during ultra-high cooling, developed in researches presented in this paper, allows researchers to estimate the results of applying in reality certain cooling conditions. This model will help developers of bulk amorphous alloys in checking if are ensured conditions to obtain an amorphous alloy with fewer experimental tests, less time and low expenses.
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49

Xu, XiaoLong, Hua Hou, Yuhong Zhao, and Feng Liu. "Preparation of bulk crystallite alloys by rapid quenching of bulk undercooled melts." Materials Science and Technology 34, no. 1 (July 30, 2017): 79–85. http://dx.doi.org/10.1080/02670836.2017.1358471.

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50

Lowe, Terry C., Ruslan Z. Valiev, Xiaochun Li, and Benjamin R. Ewing. "Commercialization of bulk nanostructured metals and alloys." MRS Bulletin 46, no. 3 (March 2021): 265–72. http://dx.doi.org/10.1557/s43577-021-00060-0.

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