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Journal articles on the topic '(Ni)3(Al,X)'

Author: Grafiati
Published: 6 September 2023

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1

SHEN, DIAN HONG, HUA LU, XINGFANG WU, NATALIA FROUMIN, and MICHA POLAK. "WETTABILITY AND MICROSTRUCTURES OF Ni-Al/TiCx SYSTEM." International Journal of Modern Physics B 16, no. 01n02 (January 20, 2002): 19–24. http://dx.doi.org/10.1142/s0217979202009408.

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Wettability and microstructures of Ni-Al/TiC x composites have been studied by measuring the wettability contact angle using the "sessile drop" method, and by observation using a scanning electron microscope (SEM) and an analytical transmission electron microscope (ATEM), together with an energy dispersive X-ray spectrometer (EDS). The equilibrium contact angle of Ni-Al alloys on TiC x (X = 0.7-1) vs. Ni content showed that the wetting angle depends on the concentration of C in TiC x. The results agreed with the observation of morphology at the interfaces between the hard phase skeleton of TiC x (x = 0.7, 0.9) and metallic phases. The concentration distance plot for Ti , and Ni across the interface of Ni 3 Al/TiC 0.7 showed that an extensive area of intermetallic compounds can be observed at the Ni 3 Al/TiC 0.7 interface. The microstructure analysis suggested that Ti in TiC 0.7 is easier to dissolve into the molten alloy than that in TiC 0.9. Some periodic zigzag fringes were also observed in the interface between metallic phase and carbides in the sample of Ni 3 Al/TiC 0.7. The formation of this periodic zigzag fringe, which may be a growth zone of a new Ti-Ni-Al phase, would occur during the initial stage of solidification in the samples obtained by infiltration. This behavior in the interface of Ni-Al/TiC x composite would affect their strength, creep resistance at elevated temperatures and low-temperature toughness.
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2

FENG, LIN, WENXING ZHANG, ENKE LIU, WENHONG WANG, and GUANGHENG WU. "MARTENSITIC TRANSFORMATION AND MAGNETIC PROPERTIES OF NiMnAl:Fe, Co FERROMAGNETIC SHAPE MEMORY ALLOYS." Functional Materials Letters 06, no. 06 (November 27, 2013): 1350050. http://dx.doi.org/10.1142/s1793604713500501.

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A series of Ni 50-x Fe x Mn 34 Al 16(0 ≦ x ≦ 18) and Ni 38 Fe 12-z Co z Mn 34 Al 16(3 ≦ z ≦ 6) ribbons were prepared by the melt-spinning method. With Fe substitution for Ni in Ni 50 Mn 34 Al 16 ribbons, the magnetization of the austenitic phase increases greatly while that of the martensitic phase increases little. Thus, in the magnetic field of 5 T a large magnetization change (22 Am2/kg) during the martensitic transformation is observed in Ni 38 Fe 12 Mn 34 Al 16 ribbon. The effect of Fe substitution for Ni on the magnetic modulation was investigated, which is attributed to the change of the magnetic interaction between Mn – Mn atoms. By substituting Co for Fe in Ni 38 Fe 12 Mn 34 Al 16 ribbons, a magnetic-field-induced martensite-austenite transformation is observed in Ni 38 Fe 9 Co 3 Mn 34 Al 16 ribbon.
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3

Myoujin, Kenichi, Takashi Ogihara, Koji Nakane, and Nobuo Ogata. "Synthesis and Characterization of Li[Ni(1/3-x)Mn(1/3-x)Co(1/3-x)Mx]O2(M=Fe,Mg,Al) Particle by Aerosol Process." Key Engineering Materials 350 (October 2007): 203–6. http://dx.doi.org/10.4028/www.scientific.net/kem.350.203.

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Spherical Li[Ni(1/3-x)Mn(1/3-x)Co(1/3-x)Mx]O2 (M=Fe, Mg, Al) precursor powders were synthesized by ultrasonic spray pyrolysis using aqueous solution of metal nitrate. X-ray diffraction (XRD), scanning electron microscope (SEM), BET method using N2 adsorption analysis and Battery tester were used for determination of the composition, morphology, particle size, surface area and electrochemical properties. SEM observation showed that the size of as-prepared particles were about 0.9 μ with narrow size distribution. The crystal phase of Li[Ni(1/3-x)Mn(1/3-x)Co(1/3-x)Mx]O2 (M=Fe, Mg, Al) was resulted in layered rock salt structure with R3m space group by calcinations at 1023 K for 10 h. No impurity-related peaks are observed from the XRD pattern with various doping metals. Mg and Al doped Li(Ni1/3Co1/3Mn1/3)O2 showed very good cycling stability. The Mg substitution for Ni led to the most excellent. On the other hand, the capacity degradation during cycling was observed by Fe substitution for Mn doped Li(Ni1/3Co1/3Mn1/3)O2.
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4

Chakravorty, S., and D. R. F. West. "Constitution of Ni3Al–Ni3Mo–Ni3W section of Ni–Al–Mo–W system." Materials Science and Technology 2, no. 10 (October 1, 1986): 989–96. http://dx.doi.org/10.1179/026708386790328119.

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5

Blinov, A. M., V. K. Portnoy, S. D. Kaloshkin, and I. A. Tomilin. "Formation of Ni-Al and Ni-Al-X Phases by Mechanical Alloying." Journal of Metastable and Nanocrystalline Materials 20-21 (July 2004): 151–56. http://dx.doi.org/10.4028/www.scientific.net/jmnm.20-21.151.

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6

Tixier, S., P. Böni, and H. Van Swygenhoven. "Hardness enhancement of sputtered Ni 3 Al/Ni multilayers." Thin Solid Films 342, no. 1-2 (March 1999): 188–93. http://dx.doi.org/10.1016/s0040-6090(98)01495-3.

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7

Narasimhan, Tiruppatur Subramaniam Lakshmi, Dieter Kath, Egbert Wessel, Torsten Markus, and Klaus Hilpert. "Knudsen effusion mass spectrometric studies of the Al–Ni system: Thermodynamic properties over {AlNi + Al3Ni2} and {Al3Ni2 + Al3Ni}." International Journal of Materials Research 97, no. 6 (June 1, 2006): 802–7. http://dx.doi.org/10.1515/ijmr-2006-0129.

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Abstract Vaporisation studies on Al–Ni alloys with x(Ni) = 0.43, 0.42, 0.35, and 0.32 were carried out by Knudsen effusion mass spectrometry. Partial pressure-temperature relations of Al(g) over the two phase regions {AlNi + Al3Ni2} and {Al3Ni2 + Al3Ni} were determined in the temperature ranges 1104 – 1278 K and 1021 –1122 K, respectively. The corresponding equations are log(p(Al)/Pa) = –(20 039 ± 84)/T(K) + (13.464 ± 0.070) for {AlNi + Al3Ni2} and log(p(Al)/Pa) = – (16 836 ± 235)/T(K) + (11.345 ± 0.219) for {Al3Ni2 + Al3Ni}. The vaporisation reactions, Al3Ni2.025(s) = 2.6436AlNi0.766(s) + 0.3564Al(g) and Al3Ni(s) = 0.572Al3Ni1.747(s) + 1.284Al(g) were evaluated and subsequently the enthalpy and Gibbs energy of formation of Al3Ni1.747(s) were derived.
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8

Ovcharenko, V. E., Sergei Grigorievich Psakhye, and E. N. Boyangin. "Bulk Nanostructured Ni3Al Intermetallic and Ni3Al-Base Alloy." Applied Mechanics and Materials 682 (October 2014): 210–15. http://dx.doi.org/10.4028/www.scientific.net/amm.682.210.

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We show here that Ni3Al compound which is widely used as the base metal for advanced multipurpose hot-resistant alloys may be efficiently bulk nanostructured for improving its physical and strength characteristics. Developing the nanostructured component in the bulk of the intermetallic compound is achieved by plastic deformation of an SHS product during its synthesis and crystallization under conditions of thermal explosion of nickel/aluminum powder mixture of stoichiometric composition. It was shown that the nanosize component is formed on the basis of intermetallic Ni3Al synthesized by SHS under hot forging conditions from nickel/aluminum powder mixed with an inert binder component. Developing the nanosize structural components improves strength of the intermetallic alloy.
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9

KIM, Y. W., G. A. WHITE, R. REIBEL, and R. J. SMITH. "ALLOY FORMATION OF ULTRATHIN Ni FILMS ON Al(111) SURFACE AT ROOM TEMPERATURE." Surface Review and Letters 06, no. 05 (October 1999): 781–86. http://dx.doi.org/10.1142/s0218625x99000792.

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The growth characteristics of ultrathin Ni films deposited on Al(111) surfaces at room temperature have been studied using high energy ion scattering/channeling (HEIS), X-ray photoelectron spectroscopy (XPS) and low energy ion scattering (LEIS). Ion channeling results show that Ni atoms deposited on the Al(111) surface react with Al substrate atoms to form two different Ni–Al alloys between 0 and 5.5 ML of Ni coverage. Alloy phases of Ni 2 Al 3 up to 1.5 ML and NiAl up to 5.5 ML were determined by XPS peak analysis. At higher Ni coverage, LEIS and XPS spectra suggest that islands of Ni metal were formed on the surface. Diffusion of Ni into the Al substrate or segregation of Al to the surface was observed during the alloy formation. The Ni 2 Al 3 phase was apparently transformed into the NiAl phase by the additional Ni deposition, and the islands of Ni metal formed on the Al-rich surface of the NiAl alloy.
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10

Zhang, Li Peng, Xian Jin Yu, Zhi Wei Ge, Yun Hui Dong, and Dang Gang Li. "Co-Deposition of Al–Ni Alloy in NiCl2-AlCl3-1-ethyl-3-methylimidazolium Bromide ([EMIM]Br) Ionic Liquid." Applied Mechanics and Materials 121-126 (October 2011): 65–69. http://dx.doi.org/10.4028/www.scientific.net/amm.121-126.65.

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Al-Ni Alloys were obtained from NiCl2-AlCl3-1-ethyl-3-methylimidazolium bromide ([EMIM]Br) ionic liquid at room temperature. The analysis of Al-Ni alloys that co-deposited at different potentials for 2h were performed using Scanning Electron Microscopy (SEM) and X-ray diffraction analysis (XRD). It appears that Ni has been rapidly solidified in the alloys and homogeneous Al-Ni alloys can be obtained at room temperature. As increasing the overpotential, the amount of Ni in the alloys was decreased whereas the amount of Al was increased. The chloride pitting potentials of alloys with the molar ratio of NiCl2/AlCl3/[EMIM]Br 0.03:2:1 was approximately 0.3 V more than pure Al.
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11

Zhang, Jian, Qiang Guo Luo, Qiang Shen, and Lian Meng Zhang. "Diffusion Mechanism and Kinetics of Diffusion Bonded Mg/Ni/Al Joint." Key Engineering Materials 616 (June 2014): 286–90. http://dx.doi.org/10.4028/www.scientific.net/kem.616.286.

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Mg and Al were bonded successfully by means of diffusion bonding using Ni interlayer. The microstructure, diffusion mechanism and regulation of atom diffusion were investigated by means of scanning electron microscopy (SEM), X-ray diffraction (XRD) and electron probe microanalysis analysis (EPMA). The results showed that the joints consisted of Mg-Ni interface and Al-Ni interface, and there were Mg2Ni formed in the Mg-Ni interface and Al3Ni formed in the Al-Ni interface, respectively. Diffusion activation energy of Mg and Al were lower than that of Ni in the Mg-Ni and Al-Ni interface. The thickness (x) of Mg2Ni and Al3Ni can be expressed as x2=3.97×10-4 exp (-139600/RT) (t-t0) and x2=8.62×10-3 exp (-174200/RT) (t-t0) with heating temperature (T) and holding time (t).
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12

Hanc, Artur, J. E. Frąckowiak, F. Binczyk, Grzegorz Dercz, Lucjan Pająk, and A. Tomczyk. "Structural Studies of Metallic Powders Fe-Al-X (X= Fe, Ni, Cu, Cr) Type Obtained by the Self-Decomposition Method and Electro-Magneto-Mechanical Grinding." Solid State Phenomena 130 (December 2007): 181–84. http://dx.doi.org/10.4028/www.scientific.net/ssp.130.181.

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The Fe-Al-X and Fe-Al-Ni-X (X = Fe,Ni,Cu,Cr) metallic powders obtained by the selfdecomposition method and next intensive grinding in an electro-magneto-mechanical mill were examined by X-ray powder diffraction (XRD). Morphology of powders was determined by scanning electron microscopy (SEM) whereas energy dispersive spectroscopy (EDS) was applied to identify the composition of phases. The FeAlX and FeAlNiX phases both of B2 type structure were found besides small amounts of Al(OH)3 and rest of metallic additions.
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13

Duan, J., Yu N. Osetsky, and David J. Bacon. "Atomistic Study of Self-Diffusion in Ni, Al and Ni3Al." Defect and Diffusion Forum 194-199 (April 2001): 423–28. http://dx.doi.org/10.4028/www.scientific.net/ddf.194-199.423.

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14

GE, H. L., Z. J. PENG, C. B. WANG, and Z. Q. FU. "EFFECT OF Al3+ DOPING ON MAGNETIC AND DIELECTRIC PROPERTIES OF Ni–Zn FERRITES BY "ONE-STEP SYNTHESIS"." International Journal of Modern Physics B 25, no. 29 (November 20, 2011): 3881–92. http://dx.doi.org/10.1142/s0217979211101703.

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Al 3+-doped Ni – Zn ferrites with composition of Ni 0.5 Zn 0.5( Fe 1-x Al x)2 O 4 (where x = 0, 0.012, 0.023, 0.035 and 0.045) were prepared by a method named "one-step synthesis." The magnetic and dielectric properties of the as-prepared Ni – Zn ferrites were investigated. X-ray diffraction data indicated that all the ferrite samples had a single-phase spinel structure. The addition of Al 3+ resulted in a reduction of the grain size, lattice constant, density, shrinkage and saturation magnetization of the as-prepared samples. The Curie temperatures, however, raised first and reduced later with increasing contents of Al 3+ in the samples, but still kept high values. Both the real and imaginary parts of permeability of ferrites decreased with increasing amount of Al 3+ doped before they reached peak value. As the applied frequency increased to higher than about 10 MHz, the real part of permeability of non-doped ferrite had already become lower than those of ferrites doped with Al 3+. Moreover, the doping of Al 3+ made their utility of magnetic permeability move to much higher frequency. The observed decreases in dielectric constants and dielectric loss tangent could be attributed to the decreased electron conductivity by substituting Fe 3+ with Al 3+ in the samples. The as-prepared high-performance soft magnetic materials prepared using such a simple and low-cost method will be much promising in high-frequency applications and industrialization.
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15

Ikeda, Teruyuki, A. Almazouzi, Hiroshi Numakura, M. Koiwa, W. Sprengel, and Hideo Nakajima. "Interdiffusion in Ni3Al." Defect and Diffusion Forum 143-147 (January 1997): 275–78. http://dx.doi.org/10.4028/www.scientific.net/ddf.143-147.275.

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16

Yamada, Masaaki, Hisayuki Tsunoda, Noriyoshi Matsui, Kazuhide Tanaka, and Uichiro Mizutani. "X-ray diffraction study of AlNiSi and AlNiGe alloy glasses." Journal of Non-Crystalline Solids 117-118 (February 1990): 164–67. http://dx.doi.org/10.1016/0022-3093(90)90904-z.

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17

Aihara, Tomoyasu, and Tomoyoshi Sho. "Molecular Dynamics Simulation on Deformation Dynamics of Ni and Ni3Al Single Crystals and Ni/Ni3Al Composite Crystal." Materials Transactions, JIM 40, no. 11 (1999): 1281–87. http://dx.doi.org/10.2320/matertrans1989.40.1281.

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18

Baker, I., F. S. Ichishita, V. A. Surprenant, and E. M. Schulson. "Rapidly Solidified and Annealed Powders of Ni 3 Al." Materials Characterization 39, no. 2-5 (August 1997): 455–66. http://dx.doi.org/10.1016/s1044-5803(97)00123-x.

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19

LI, YAN, ZEMIN LIU, and LI XIAO. "PHASE TRANSFORMATIONS AND MECHANICAL PROPERTIES OF NITIAL SHAPE MEMORY ALLOYS WITH EQUAL NI/TI ATOM RATIO." International Journal of Modern Physics B 24, no. 15n16 (June 30, 2010): 2423–28. http://dx.doi.org/10.1142/s0217979210065039.

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Phase transformation, microstructure and mechanical property of Ni 50- x /2 Ti 50- x /2 Al x ( x =1, 2, 3 and 4 at.%) alloys have been investigated by electrical resistance (ER) measurement, scanning electron microscope (SEM), X ray diffraction (XRD) and tensile tests. The results show that a two-step phase transformation occurs from parent phase to R phase and subsequently to martensite upon cooling, and the transformation reverses upon heating. Both the martensitic transformation and R phase transformation temperatures decrease with increasing of Al content. The microstructure analysis indicates that the NiTi - Al alloys are composed of NiTi as the predominant phase and Ti 2 Ni as the second phase mainly distributing at grain boundaries. The solid solution hardening effect of Al at room temperature has been demonstrated by the remarkable increasing of yielding strength and decreasing of tensile strain with increasing of Al content. Ni 49 Ti 49 Al 2 alloy deformed at the liquid temperature exhibits a maximum recoverable strain of 6.3%.
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20

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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21

LIU, JIANDANG, HUIMIN WENG, XIANGLEI CHEN, HUAIJIANG DU, BANGJIAO YE, WENJUAN LI, and JICHENG ZHOU. "CHARACTERIZATION OF Ni-RICH INTERMETALLIC COMPOUND Ni3Al FILMS WITH SLOW POSITRON BEAM." Modern Physics Letters B 23, no. 26 (October 20, 2009): 3097–106. http://dx.doi.org/10.1142/s0217984909021132.

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Ni -rich intermetallic compound Ni 3 Al films were deposited using the dual-target magnetron co-sputtering method. The grain-boundary and grain-size characteristics of the as-deposited and post-annealed Ni 3 Al films were investigated using a slow positron beam. The results demonstrate a distinct change of S-parameter and positron effective diffusion length L eff values as samples were annealed at different ambient atmospheres and temperatures. It shows that the positron trapping center is mainly associated with intergranular vacancies, and changes to either the vacancy cluster size or the grain size have been invoked to explain the changes of the values of the S-parameter and L eff . Ni -rich oxygen- Ni 3 Al films were also studied. All films were identified using X-ray diffraction and the results confirm the conclusion obtained by the slow positron beam.
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22

Zhang, Yang, Hongyuan Yang, Qing Liu, and Bing Bian. "MoO x ‐Doped Ordered Mesoporous Ni/Al 2 O 3 Catalyst for CO Methanation." Energy Technology 8, no. 6 (April 22, 2020): 2000165. http://dx.doi.org/10.1002/ente.202000165.

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23

Arranz, Antonio, and Carlos Palacio. "Influence of X Cation Covalence in the Formation of Ni-O-X Mixed Oxides by Reactive Ion Beam Mixing of Ni/X Interfaces." Crystals 13, no. 2 (February 17, 2023): 345. http://dx.doi.org/10.3390/cryst13020345.

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The reaction of the Ni/X interfaces (X = Si or Cr) with O2+ ions at low energy (3 keV) was studied using X-ray photoelectron spectroscopy (XPS) and factor analysis (FA). It was found that low ion doses lead to the formation of a NiO thin film on the surface that was progressively transformed into a Ni-O-X mixed oxide with increasing the ion dose. The degree of transformation of NiO into Ni-O-X depended on the covalence of the X cation, indicating that the reaction was influenced by chemical driving forces. For strong covalent cations (Si and Al), NiO was completely transformed into Ni-O-X at ion doses above 1.8 × 1017 ions/cm2, whereas for ionic cations (Cr) the transformation was incomplete. The ionicity of Ni atoms in the Ni-O-X mixed oxide increased with the increase in the covalence of X cation, and the features of the Ni 2p core level, characteristic of bulk NiO which were attributed to non-local screening, disappeared.
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24

Morales, Ruddy, Cristian H. Campos, J. L. G. Fierro, Marco A. Fraga, and Gina Pecchi. "Perovskite as nickel catalyst precursor – impact on catalyst stability on xylose aqueous-phase hydrogenation." RSC Advances 6, no. 72 (2016): 67817–26. http://dx.doi.org/10.1039/c6ra13395a.

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Precursors materials with formula, La1−xCexAl0.18Ni0.82O3 (x = 0.0, 0.1, 0.5, 0.7), were successfully used as precursors to prepare Ni nanoclusters to be used as catalysts in the hydrogenation of xylose to xylitol.
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25

Yang, Zi Jie, Hui Yu, Li Wen Ma, Xiao Li Xi, and Yun He Zhang. "Removal of Metal Impurities from the Spent Hydroprocessing Catalyst and Acid Leaching Kinetics of Aluminum." Materials Science Forum 993 (May 2020): 1438–44. http://dx.doi.org/10.4028/www.scientific.net/msf.993.1438.

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The impurity metal of Al in spent hydroprocessing catalyst (Mo-Ni/Al2O3) was removed by HCl, and the metals of Mo and Ni were preliminarily enriched. The results show that the leaching efficiency of Al was 88.62%, and the leaching efficiency of Mo and Ni were 16.32% and 28.74%, respectively. The results were achieved under optimal leaching conditions: the particle size was 150 μm, the concentration of HCl was 4 mol/L, the leaching temperature was 90 °C, and the leaching time was 120 min. The kinetics of the leaching behavior of Al showed that the acid leaching reaction of Al was in accorded with the equation 1-2/3X-(1-X) 2/3=K2t, R2=0.97734, which was controlled by internal diffusion. X-ray diffraction analysis of the leaching residue revealed the existence of residual metals Mo(MoO3, MoO2(ClO4)2)and Ni(NiS). The separation of Al from Mo and Ni has been preliminarily realized, which is conducive to further efficient recovery of Mo and Ni.
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26

Chen, T. P., X. Yang, U. Tipparach, A. Zhou, B. Chen, Q. Y. Chen, and J. T. Wang. "Structure and Transport Studies on PrBa2(Cu1-xMx)3O7: M = Al, Fe, and Ni." International Journal of Modern Physics B 17, no. 18n20 (August 10, 2003): 3655–60. http://dx.doi.org/10.1142/s0217979203021563.

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We have fabricated metal doped PrBa 2 Cu 3 O 7 (PBCO), i.e. PrBa 2( Cu 1-x M x)3 O 7 (PBCMO) with M = Al , Fe, and Ni, and x = 0.05, 0.10, 0.15, and 0.20. X-ray data indicate no significant second phase for Ni-doped samples until 15% doping level is reached. No second phase was found in Al- and Fe-doped samples up to the 20% doping level. All the doped samples are in orthorhombic structure and their lattice parameters are very close to those of YBa 2 Cu 3 O 7-δ (YBCO). However, for Al or Fe doped samples the difference in lattice parameters a-b has decreased from that of PBCO. At 77 K the electrical resistivity for Al- or Fe-doped samples is several orders in magnitude higher than that of PBCO. Therefore these compounds may be better buffer-layer materials for YBCO superconducting electronic circuits and devices.
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27

SCHANK, C., F. JÄHRLING, U. TEGEL, C. GEIBEL, A. GRAUEL, A. BÖHM, R. BORTH, et al. "U(Pd1−xNix)2Al3: AN ALLOY BETWEEN TWO HEAVY-FERMION SUPERCONDUCTORS." International Journal of Modern Physics B 07, no. 01n03 (January 1993): 46–49. http://dx.doi.org/10.1142/s0217979293000123.

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We present and analyze measurements of the electrical resistivity, the dc- and ac-susceptibility and the specific-heat of the quasi-binary alloy U ( Pd 1− x Ni x )2 Al 3 in the temperature range from 0.3K to 300K. All investigated properties indicate a continuous change from UPd 2 Al 3 to UNi 2 Al 3, with the exception of superconductivity, which dissappears for 0.12 ≤ x ≤ 0.95. The results stress the importance of crystal field effects.
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28

Krajewski, Witold K. "Determination of Al Site Preference in L12 TiZn3 - Base Trialuminides." Materials Science Forum 508 (March 2006): 615–20. http://dx.doi.org/10.4028/www.scientific.net/msf.508.615.

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The atoms site preference in the Al3Ti-Zn system has been studied using H. Rietveld method. The L12 Ti(Al, Zn)3 particles evolve in a ZnAl25 melt from the L12TiZn3 particles in the ZnTi4 master alloy. It is found that Zn is replaced by Al during the transformation TiZn3 → Ti(Al, Zn)3. In the evolving fcc L12 Ti(Al, Zn)3 phase Ti occupies (0, 0, 0) position while Al and Zn occupy (0, 0.5, 0.5) position, similarly to Al and X in the Al3Ti-X systems, where X = Ni, Cr, Mn, Cu, Ag, Pd [1, 2].
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29

Barmak, K., S. W. Banovic, C. M. Petronis, D. F. Susan, and A. R. Marder. "Structure of electrodeposited graded composite coatings of Ni–Al–Al 2 O 3." Journal of Microscopy 185, no. 2 (February 1997): 265–74. http://dx.doi.org/10.1046/j.1365-2818.1997.d01-606.x.

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30

Sato, Eiichi, Koichi Kitazono, and Kazuhiko Kuribayashi. "Plastically Accommodated Creep in Al-Al3Ni Composite." Materials Transactions, JIM 37, no. 3 (1996): 340–44. http://dx.doi.org/10.2320/matertrans1989.37.340.

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31

Fritsch, Veronika, Chien-Lung Huang, Nadezda Bagrets, Kai Grube, Sarah Schumann, and Hilbert v. Löhneysen. "Magnetization and specific heat of CePd1 − x Ni x Al." physica status solidi (b) 250, no. 3 (February 27, 2013): 506–10. http://dx.doi.org/10.1002/pssb.201200931.

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32

Puspitasari, P., R. Fauzan, T. L. Ginta, M. Mustapha, and D. Puspitasari. "Morphology of aluminium with nickel addition on sand casting process." Journal of Achievements in Materials and Manufacturing Engineering 1, no. 87 (March 1, 2018): 13–17. http://dx.doi.org/10.5604/01.3001.0012.0734.

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Purpose: his research aimed to examine the morphology, elemental changes, and phase in the aluminium cast alloys with variations in nickel addition of 1%, 2% and 3%. Design/methodology/approach: Aluminium 98% was melted in sand casting process. The sand casting process was operated at 7000C and atmospheric pressure. The addition of nickel contain of 92.19% of its element. Specimens consist of 4 pieces Al-Ni with the size of 1 x 1 x 0.5 cm for morphological testing, while for phase identification testing consist of 4 pieces Al-Ni with the size of 1 x 1 x 2 cm. The morphological testing was performed using FEI Inspect S50 Scanning Electron Microscope (SEM) and the phase characterisation was conducted using Nikon ME5 Optical Microscope. Findings: The results showed that the addition of 1% nickel in the aluminium cast product could affect the morphology in granular shape with as similar size, at 2% nickel addition also has granular shape, while at 3% of nickel addition, the morphology of Al-Ni was in elongated shape. Phase identification of Al-Ni cast alloy shows that there were Al matrix with nickel that spread in grain boundary of Al. By increasing the percentage of nickel, it shows that the nickel dominated the grain boundary of Al. These results shows that Al-Ni alloy can be produced at simple route on sand casting process. Research limitations/implications: Sand casting process with 80% silica sand, 10% bentonite, 5% water. Raw material of aluminium contains of 92-99% of purity. Nickel as addition element contain of 90-92% purity. Practical implications: The addition of nickel should be prepared wisely in term of the calculation of alloying treatment because it will effect the mechanical properties of Al alloy itself. This research can be improved by varying the temperature of casting process, variation of nickel percentage, and observation of mechanical properties of Al-Ni alloy. Originality/value: Simple route of making Al-Ni alloy using sand casting method in laboratory and also the observation of nickel addition in aluminium matrix as the result of casting product.
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33

Breuer, J., A. Grün, F. Sommer, and E. J. Mittemeijer. "Enthalpy of formation of B2-Fe1−x Al x and B2-(Ni,Fe)1−x Al x." Metallurgical and Materials Transactions B 32, no. 5 (October 2001): 913–18. http://dx.doi.org/10.1007/s11663-001-0077-8.

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34

Murch, Graeme E., and Irina V. Belova. "Chemical Diffusion in Ni3Al." Defect and Diffusion Forum 194-199 (April 2001): 541–46. http://dx.doi.org/10.4028/www.scientific.net/ddf.194-199.541.

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35

Fujiwara, K., and Z. Horita. "Intrinsic Diffusion in Ni3Al." Defect and Diffusion Forum 194-199 (April 2001): 565–70. http://dx.doi.org/10.4028/www.scientific.net/ddf.194-199.565.

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36

Chiba, Akihiko, Shuji Hanada, Sadao Watanabe, Takeshi Obana, Kazuo Tanosaki, and Masayoshi Fujita. "Ductility of Undoped Ni3Al." Materials Transactions, JIM 33, no. 5 (1992): 503–8. http://dx.doi.org/10.2320/matertrans1989.33.503.

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37

Cairney, J. M., T. S. Rong, I. P. Jones, and R. E. Smallman. "Intermediate temperature creep mechanisms in Ni 3 Al." Philosophical Magazine 83, no. 15 (January 2003): 1827–43. http://dx.doi.org/10.1080/1478643031000081293.

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38

LIANG, SEN, XIAO ZHANG, HAIBO LI, MIN LUO, JIN LI, LIJUN HE, and JIANFENG YANG. "FABRICATION AND CHARACTERIZATION OF Ni–Mn–Si–Al–O NTC THERMISTOR AND ITS APPLICATION AS TEMPERATURE WIRE SENSOR." Functional Materials Letters 06, no. 04 (August 2013): 1350039. http://dx.doi.org/10.1142/s1793604713500392.

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A series of Al 2 O 3 substituted manganese oxide ceramic compounds, Ni 0.6 Si 0.2 Mn 2.2-x Al x O 4(0 ≤ x ≤ 0.6), were prepared by solid-state reaction route. The phase composition, microstructure, and electrical properties of compounds were studied. The results revealed that all the compounds were composed of cubic spinel structure without any other oxides. Besides they exhibited a linear relationship between logarithm of electrical resistivity (ln ρ) and reciprocal of absolute temperature (1/T) over a temperature ranging from room temperature to 300°C, which indicated a negative temperature coefficient (NTC) characteristic. The B25/85 constant was found to increase with the increase of Al 2 O 3 content. The B25/85 values of the NTC Ni 0.6 Si 0.2 Mn 2.2-x Al x O 4 thermistors for x = 0,0.1,0.2,0.3,0.4, and 0.6 were 4581, 4612, 4680, 4875, and 5089 K, respectively. Finally, a new method to produce one meter long continuous fire wire sensors was also proposed.
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39

Belova, Irina V., and Graeme E. Murch. "Analysis of Diffusion in Ni3Al and Ni3Ge." Defect and Diffusion Forum 143-147 (January 1997): 321–26. http://dx.doi.org/10.4028/www.scientific.net/ddf.143-147.321.

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40

RASHIDI, A. M., and A. AMADEH. "GROWTH KINETICS OF ALUMINIDE LAYERS ON NANOCRYSTALLINE NICKEL." International Journal of Modern Physics: Conference Series 05 (January 2012): 654–60. http://dx.doi.org/10.1142/s2010194512002590.

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In this research, the simultaneous growth of Al 3 Ni 2 and Al 3 Ni on nanocrystalline nickel was investigated. Nanocrystalline nickel samples with mean grain size of about 25 nm were prepared by direct current electroplating. The samples were aluminized for different durations by pack cementation method at 500, 550 and 600 °C. The aluminide phases were identified by SEM, EDS and XRD. In contrast to reported results suggesting the formation single layer of Al 3 Ni 2 phase on coarse grained nickel, it was observed that long time aluminizing of nanocrystalline nickel resulted in the formation and simultaneous growth of two distinct layers of Al 3 Ni 2 and Al 3 Ni phases. The growth of both phases followed the parabolic growth kinetics, but the growth rate constant of Al 3 Ni 2 was much greater than Al 3 Ni layer. Also, the simultaneous growth of Al 3 Ni 2 and Al 3 Ni was modeled. Based on this model, the activation energy of the coating growth (total Al 3 Ni 2 and Al 3 Ni layers) was determined as about of 178 kJ/mol.
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41

Ootoshi, Y., K. Fujiwara, Z. Horita, and M. Nemoto. "Formation of Ni5Al3 Phase in Ni3Al/NiAl Diffusion Couples." Materials Transactions, JIM 39, no. 1 (1998): 225–29. http://dx.doi.org/10.2320/matertrans1989.39.225.

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42

Belova, Irina V., and Graeme E. Murch. "Analysis of Diffusion Mechanisms in Ni3Al, Ni3Ge and Ni3Ga." Defect and Diffusion Forum 177-178 (February 2000): 59–68. http://dx.doi.org/10.4028/www.scientific.net/ddf.177-178.59.

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43

Zuo, Kai Hui, Dong Liang Jiang, Qing Ling Lin, Yu Ping Zeng, and Zhong Ming Chen. "Mechanical Properties of (Al2O3+Ni) and (Al2O3+Ni)/Ni Laminated Materials." Key Engineering Materials 353-358 (September 2007): 1447–50. http://dx.doi.org/10.4028/www.scientific.net/kem.353-358.1447.

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(Al2O3+Ni) and (Al2O3+Ni)/Ni laminated materials were prepared by tape casting and hot pressing sintering. The mechanical properties of (Al2O3+20wt%Ni) laminated composites were higher than those of (Al2O3+50wt%Ni) composites and Al2O3 sample. The strengthening in the (Al2O3+Ni) composites mainly results from microstructure refinement of the alumina grain size, cracks bridging and crack deflection by the Ni particles. Results showed that the strength and fracture toughness of (Al2O3+Ni)/Ni laminated materials were higher than those of Al2O3/Ni laminated materials with the same layer numbers and thickness ratio. The good mechanical properties of (Al2O3+Ni) and (Al2O3+Ni)/Ni laminated materials result from the second phase of Ni particles in Al2O3 layers.
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44

Karthikeyan, B., V. Raja, N. Rajamanickam, and S. P. Bagare. "On the Franck-Condon factors and R-centroids of the astrophysically interesting molecule CS." Serbian Astronomical Journal, no. 175 (2007): 25–32. http://dx.doi.org/10.2298/saj0775025k.

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In molecular astrophysics, the Franck-Condon (FC) factors and r-centroids are essential for the interpretation of spectral intensities in terms of emitting astrophysical source conditions. They have been evaluated for the band systems a 3?r - X 1?+, d3?ni - X 1?+- X 1?+, e 3?- - X 1?+, A' 1?+ - X 1?+ and d3?ni and - a 3?r of astrophysical molecule CS. The physical and astrophysical significances of our evaluated FC factors and r-centroids are discussed. The FC factor values of a - X system have been compared with the values of FC factors reported by Reddy et al. (2003).
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45

Mohammed, Noor M., Farah AH Kadhim, Aseel A. Hammood, and Ashour H. Dawood. "Ciprofloxacin Based on Carrier Double Layered Hydroxide Nano-particles of Fe+3/Fe+2, Fe+3/Ni+2, Al+3/Fe+2, and Al+3/Ni+2 Ions." International Journal of Drug Delivery Technology 10, no. 01 (March 25, 2020): 119–26. http://dx.doi.org/10.25258/ijddt.v10i1.26.

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The double-layered hydroxide nano-particles compounds with ciprofloxacin drug were carried out by preparation of the double layered hydroxide (DLH) of M+3/M+2 ions for selective ions. The ciprofloxacin drug was inserted between them. The resulted compounds were characterized by X-Ray diffraction (XRD), scanning electron microscope (SEM), atomic force microscope (AFM), and Fourier Transform Infrared (FT-IR) spectroscopy; the antibacterial studied done by using the gram (+) and gram (-) pigments.
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46

STEGLICH, F., C. GEIBEL, A. LOIDL, G. SPARN, C. D. BREDL, and R. CASPARY. "HEAVY FERMIONS — THEIR MAGNETISM AND SUPERCONDUCTIVITY." International Journal of Modern Physics B 07, no. 01n03 (January 1993): 2–8. http://dx.doi.org/10.1142/s0217979293000020.

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Heavy-fermion compounds are ideally suited to study cooperative phenomena in highly correlated electron systems. We discuss local-moment magnetism and heavy-fermion band magnetism in the exemplary systems CeCu 2 Ge 2 and Ni-rich Ce(Cu 1− x Ni x )2 Ge 2, respectively. In addition, the coexistence of long-range antiferromagnetic order and heavy-fermion superconductivity in UM 2 Al 3 (M: Ni, Pd) will be addressed.
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47

Grushko, B., and S. Balanetskyy. "X-ray powder diffraction data for Al73.5Ni18.5Re8 orthorhombic phase." Powder Diffraction 23, no. 3 (September 2008): 251–54. http://dx.doi.org/10.1154/1.2957883.

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A ternary phase was revealed in Al-Ni-Re in a small compositional range around Al73.5Ni18.5Re8. Using powder X-ray diffraction and electron diffraction, it was found to have an orthorhombic structure with a=10.048(3) Å, b=15.423(8) Å, and c=8.367(3) Å.
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48

Kitashima, Tomonori. "Thermodynamic Analysis of the Effects of Alloying Elements on the Stacking Fault Energy in Ruthenium-Bearing Nickel Alloys." Advanced Materials Research 1119 (July 2015): 580–84. http://dx.doi.org/10.4028/www.scientific.net/amr.1119.580.

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The effects of Al, Co, Re, and Ru on the stacking fault energy in Ni alloys were analyzed using computational thermodynamics. The effects of adding up to 5 at% Re or Ru to a Ni-15at%Co system were found to be weak at 300 °C, 700 °C, and 900 °C. However, Al addition decreased the stacking fault energy in a Ni-15at%Co-Xat%Ru system, where X = 0, 3, 5. In addition, this decrease in the stacking fault energy due to Al addition became more significant as the amount of Ru increased. Furthermore, in Ni–Co–Al–Ru alloys containing 9at%Al, the addition of 5at%Ru decreased the stacking fault energy as much as the addition of 12.5at%Co at 900 °C. The effects of Co and Ru addition on the γ/γ’ microstructure of Ni-based superalloys were also discussed.
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49

LIU, PENG, WEI GUO, and HUI LUO. "A STUDY ON MICROSTRUCTURE CHARACTERISTICS OF IN SITU FORMED TiC REINFORCED COMPOSITE COATINGS." Surface Review and Letters 19, no. 02 (April 2012): 1250016. http://dx.doi.org/10.1142/s0218625x12500163.

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In situ synthesized TiC reinforced composite coating was fabricated by laser cladding of Al-Ni-Cr-C powders on titanium alloys, which can greatly improve the surface performance of the substrate. In this study, the Al-Ni-Cr-C laser-cladded composite coatings have been researched by means of X-ray diffraction, scanning electron microscope (SEM) and electron probe micro-analyzer (EPMA). There was a metallurgical combination between the Al-Ni-Cr-C laser-cladded coating and the Ti-6Al-4V substrate, and the micro-hardness of the Al-Ni-Cr-C laser-cladded coating was in the range of ~1200–1450 HV0.2, which was ~3–4 times higher than that of Ti-6Al-4V substrate. Furthermore, the reinforcement of the Al-Ni-Cr-C laser-cladded coating were mainly contributed to the action of the TiC , Ti3Al , Cr7C3 , Al8Cr5 phases and the solution strengthening.
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50

Hsu, Li-Shing, K. L. Tsang, and S. C. Chung. "Resonant Valence-Band Satellites at the Ni-3p Edge of Ni3Al, Ni3Ga and Ni3In." International Journal of Modern Physics B 12, no. 26 (October 20, 1998): 2757–67. http://dx.doi.org/10.1142/s0217979298001605.

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Valence-band photoemission sspectra of Ni 3 Al , Ni 3 Ga and Ni 3 In were measured with synchrotron radiation at photon energies around the Ni-3p core excitation threshold. The valence-band satellites are resonantly enhanced. The number of holes per Ni atom in the Ni-d band for Ni 3 Al , Ni 3 Ga and Ni 3 In is estimated to be 0.37, 0.30 and 0.34, respectively. The self-energy correction due to the configuration interaction is 0.72, 0.71 and 0.72 eV, respectively, for Ni 3 Al , Ni 3 Ga and Ni 3 In . The Fano parameters and the effective Coulomb interactions between two 3D holes for these intermetallic compounds are determined.
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