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Journal articles on the topic 'Peritectic'

Author: Grafiati

Published: 4 June 2021

Last updated: 14 February 2022

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1

Su, Yan Qing, Dong Mei Liu, Xin Zhong Li, Liang Shun Luo, Jing Jie Guo, and H. Z. Fu. "Microstructure Evolution of Directionally Solidified Al-25at.%Ni Peritectic Alloy." Advanced Materials Research 79-82 (August 2009): 1655–58. http://dx.doi.org/10.4028/www.scientific.net/amr.79-82.1655.

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Microstructure evolution of peritectic Al-25at.%Ni alloy during directional solidification with pulling velocity ranging from 2 to 500m/s is investigated. The directional solidified alloy is composed of Al3Ni2, Al3Ni phase and eutectic (Al3Ni+Al) phase. When pulling velocity ranges from 2 to 5m/s, Al3Ni phase grows into an integral matrix. Majority of primary Al3Ni2 is consumed by peritecti reaction and transformation behind the peritectic interface with pulling velocity ranging from 2 to 20 m/s. While pulling rate increases, major Al3Ni phase direct solidifies from liquid. With cooling rate increasing, Al3Ni2 phase content firstly decreases and then increases, while the Al3Ni phase content decreases throughout.

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2

Zhu, Xin Hua, Li Huang Zhu, Yu Liu, and Tian Long Liu. "Peritectic-Steel Mold Fluxes." Advanced Materials Research 567 (September 2012): 75–78. http://dx.doi.org/10.4028/www.scientific.net/amr.567.75.

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As peritectic steel is crack sensitive steel, peritectic-steel mold flux needs a higher performance requirement, In this paper, it is analyzed in detail that various properties of peritectic steel mold flux have effects on the quality of peritectic steel billet .

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3

Chen, Y. Z., F. Liu, G. C. Yang, and Y. H. Zhou. "Nonequilibrium effects of primary solidification on peritectic reaction and transformation in undercooled peritectic Fe–Ni alloy." Journal of Materials Research 25, no. 6 (June 2010): 1025–29. http://dx.doi.org/10.1557/jmr.2010.0156.

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Applying the glass fluxing method, a peritectic Fe–Ni alloy with a composition of Fe–4.35 at.% Ni was undercooled. It was found that when the initial melt undercooling (ΔT) is smaller than 130 K, the overall thickness of the peritectic phase formed in peritectic reaction (PR) and peritectic transformation (PT) decreases as ΔT increases. The nonequilibrium effects of the primary solidification on PR and PT in the undercooled peritectic Fe–Ni alloys were illuminated. With increasing ΔT, since the driving forces for PR and PT change slightly, the decrease of the overall thickness of the peritectic phase formed in PR and PT can be mainly ascribed to the reduced transformation time for PT.

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4

Pu, Dazhi, Guanghua Wen, Dachao Fu, Ping Tang, and Junli Guo. "Study of the Effect of Carbon on the Contraction of Hypo-Peritectic Steels during Initial Solidification by Surface Roughness." Metals 8, no. 12 (November 23, 2018): 982. http://dx.doi.org/10.3390/met8120982.

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In the continuous casting process, the shrinkage of the peritectic phase transition during the initial solidification process has an important influence on the surface quality of peritectic steel. The initial solidification process of 0.10C%, 0.14C%, and 0.16C% peritectic steels was observed in situ by a high temperature laser confocal microscope, and the contraction degree during initial solidification was characterized by surface roughness. The results showed that under the cooling rate of 20 °C/s, the surface roughness value Ra(δ/γ) of 0.10C% peritectic steel was 32 μm, the Ra(δ/γ) value of 0.14C% peritectic steel was 25 μm, and the Ra(δ/γ) value of 0.16C% peritectic steel was 17 μm. With increasing carbon content, the contraction degree of the δ→γ transformation decreased, and the value of the surface roughness Ra(δ/γ) declined. Therefore, surface roughness can characterize the contraction degree of the δ→γ transformation in the initial solidification process of peritectic steel under the condition of a large cooling rate.

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5

Guo, Jun Li, Guang Hua Wen, Ping Tang, and Jiao Jiao Fu. "Analysis of Peritectic Transformation Contraction of 304 Stainless Steel Using Surface Roughness." Materials Science Forum 1005 (August 2020): 10–17. http://dx.doi.org/10.4028/www.scientific.net/msf.1005.10.

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Peritectic transformation contraction of ferrite to austenite plays an important role in the formation of cracks for steels. In order to evaluate the peritectic transformation contraction of steels at the initial solidification, the solidification of 304 stainless steel under different cooling rates were carried out by using high temperature laser confocal microscopy, and then the surface roughness and peritectic transformation contraction were analysed in combination with the microstructure of solidified steel. The result shows that the solidification model of 304 stainless steel was ferrite-austenite model in the experiments, and peritectic transformation occurred during solidification. The residual ferrite in the as-cast structure were vermicular, skeletal and reticular in turn with the increase of cooling rate. The volume contraction caused by peritectic transformation resulted in wrinkles (surface roughness) appearing on the grain surface. The peritectic transformation contraction that was affected by surface roughness increased first and then decreased with cooling rate increasing, indicating the peritectic transformation contraction can be evaluated by the surface roughness.

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6

Lu, X. Y., D. Yi, and H. Chen. "A Pseudo-Binary Diagram of the (Bi,Pb)-Sr-Ca-Cu-O System." Materials Science Forum 750 (March 2013): 184–87. http://dx.doi.org/10.4028/www.scientific.net/msf.750.184.

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A pseudo-binary phase diagram of the (Bi,Pb)-Sr-Ca-Cu-O system along the Bi1.6Pb0.4Sr2Can-1CunOx line is constructed. This resulting phase diagram shows three kinds of peritectic reactions, one eutectic reaction and one peritectoid reaction. The equilibrium solid phases in this diagram are the 2201 (n=1), 2212 (n=2), 2223 (n=3) and (Sr,Ca)CuO2 (n→∝) phases. The 2201 phase is solid solution which is stable at 1≤n≤1.2. The eutectic composition point is close to the maximum solid solution composition of the 2201 phase. The temperature interval between the peritectic reaction of L + (Sr,Ca)2CuO3 + (Sr,Ca)CuO2 → 2212 and the eutectic reaction of L → 2201 + 2212 is only about 3°C. For the composition of n=3, CaO and the liquid phase are stable at temperatures above 940°C. During the cooling, these two phases react peritectically to (Sr,Ca)2CuO3. At around 890°C, (Sr,Ca)2CuO3 reacts with the liquid to produce (Sr,Ca)CuO2. At around 865°C, (Sr,Ca)2CuO3 and (Sr,Ca)CuO2 react with the liquid to produce the 2212. The 2223 phase is transformed by a peritectoid reaction of the 2212 phase and residual (Sr,Ca)2CuO3, (Sr,Ca)CuO2.

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7

Qu, Tianpeng, Deyong Wang, Huihua Wang, Dong Hou, and Jun Tian. "Effect of Magnesium Treatment on the Hot Ductility of Ti-Bearing Peritectic Steel." Metals 10, no. 10 (September 25, 2020): 1282. http://dx.doi.org/10.3390/met10101282.

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Surface cracking is a major defect in the production of continuous casting slabs of peritectic steel. The difference in crystal structure between δ phase (before peritectic transformation of steel) and γ phase (after peritectic transformation) results in volume contraction, which leads to uneven cooling of mold and thus forming slab shells with different thicknesses. Then, coupled with the concentration of local stress, surface cracking occurs on slabs. In this paper, the effect of magnesium treatment on the hot ductility of Ti-bearing peritectic steel was studied, and the characteristics of solidification structure and TiN particles were analyzed. Magnesium treatment for Ti-bearing peritectic steel could significantly improve the hot ductility of continuous casting slabs by refining the original austenite structure. After the magnesium treatment, the average grain size of the original austenite of peritectic steel decreased by about 18.7%, and the size of Mg-rich TiN particles decreased by about 41%. In addition, the minimum reduction of area at the third brittle zone after the magnesium treatment was higher than 60%, and the fracture appearance changed from intergranular fracture to ductile fracture after the treatment. The contents of Mg, Ti, O, and N in peritectic steel and the cooling conditions were adjusted reasonably to promote the formation of highly dispersed Mg-rich TiN particles with a sufficient number density and a proper size in the initial solidification stage of peritectic steel, so as to induce the high-temperature δ-ferrite nucleation. Based on the fine δ structure formed by peritectic transformation, through the use of structure heredity and the pinning effect of secondary-precipitated nano TiN particles on the austenite grain boundary, a fine and dense original austenite structure could be obtained to improve the hot ductility of peritectic steel. Industrial tests showed that through the magnesium treatment, the surface cracks of Ti-bearing peritectic steel were effectively restrained, and the corner cracks of slabs were basically eliminated.

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8

Dobler, S., T. S. Lo, M. Plapp, A. Karma, and W. Kurz. "Peritectic coupled growth." Acta Materialia 52, no. 9 (May 2004): 2795–808. http://dx.doi.org/10.1016/j.actamat.2004.02.026.

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9

StJohn, D. H. "The peritectic reaction." Acta Metallurgica et Materialia 38, no. 4 (April 1990): 631–36. http://dx.doi.org/10.1016/0956-7151(90)90218-6.

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10

Said, Rita Mohd, Mohd Arif Anuar Mohd Salleh, Norainiza Saud, Mohd Izrul Izwan Ramli, and Andrei Victor Sandu. "Solidification Behavior of Sn Cu Based Peritectic Alloys: A Short Review." Solid State Phenomena 273 (April 2018): 34–39. http://dx.doi.org/10.4028/www.scientific.net/ssp.273.34.

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Microstructure evolution that exhibit from the reaction of Sn Cu pritectic alloys become an interesting phenomenon that need to be explored since the properties of the alloys depend on their microstructures. Due to less understanding on the solidification behavior on peritectic alloys, extensive research are made on this type of alloys to gain more information regarding on the microstructure formation. This paper reviews the mechanisms on peritectic solidification on Sn Cu based peritectic alloys. The changed in peritectic microstructure due to external source such as direct current (DC) field, ultrasonic field and isothermal time are discuss respectively through this paper. The focus is made on peritectic solidification of Sn Cu based alloy since it has a promising potential for high temperature lead-free solder application.

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11

Mogeritsch, Johann P., Mehran Abdi, and Andreas Ludwig. "Investigation of Peritectic Solidification Morphologies by Using the Binary Organic Model System TRIS-NPG." Materials 13, no. 4 (February 21, 2020): 966. http://dx.doi.org/10.3390/ma13040966.

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Under pure diffusive growth conditions, layered peritectic solidification is possible. In reality, the competitive growth of the primary α-phase and the peritectic β-phase revealed some complex peritectic solidification morphologies due to thermo-solutal convection. The binary organic components Tris-(hydroxylmenthyl) aminomethane-(Neopentylglycol) were used as a model system for metal-like solidification. The transparency of the high-temperature non-faceted phases allows for the studying of the dynamic of the solid/liquid interface that lead to peritectic solidification morphologies. Investigations were carried out by using the Bridgman technic for process conditions where one or both phases solidify in a non-planar manner. Different growth conditions were observed, leeding to competitive peritectic growth morphologies. Additionally, the competitive growth was solved numerically to interpret the observed transparent solidification patterns.

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12

Wołczyński, W. "Back-Diffusion In Crystal Growth. Peritectics." Archives of Metallurgy and Materials 60, no. 3 (September 1, 2015): 2409–14. http://dx.doi.org/10.1515/amm-2015-0393.

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Abstract A model for the solute micro-segregation/redistribution is delivered. The description is associated with solidification of the peritectic alloys. The peritectic transformation is treated as the phenomenon which modifies the solute redistribution profile resulting from both partitioning and back-diffusion. The relationship allowing for the amount of peritectic phase calculation is also formulated.

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13

Dippenaar, Rian J. "Continuous Casting of Advanced Steels of Near-Peritectic Composition." Materials Science Forum 654-656 (June 2010): 17–22. http://dx.doi.org/10.4028/www.scientific.net/msf.654-656.17.

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The automotive industry is increasingly utilizing advanced high-strength steels, primarily to reduce the mass of motor vehicles. However, many of these steels fall within the peritectic composition range, which are notoriously difficult to cast by continuous casting techniques. Against this background, a brief review is given of our current understanding of the peritectic reaction as such and the subsequent peritectic phase transformations.

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14

Chen, Y. Z., F. Liu, G. C. Yang, N. Liu, C. L. Yang, and Y. H. Zhou. "Suppression of peritectic reaction in the undercooled peritectic Fe–Ni melts." Scripta Materialia 57, no. 8 (October 2007): 779–82. http://dx.doi.org/10.1016/j.scriptamat.2007.06.051.

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15

MARUYAMA, Tohru, Kiyotaka MATSUURA, Masayuki KUDOH, and Yohichi ITOH. "Peritectic Transformation and Austenite Grain Formation for Hyper-peritectic Carbon Steel." Tetsu-to-Hagane 85, no. 8 (1999): 585–91. http://dx.doi.org/10.2355/tetsutohagane1955.85.8_585.

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16

Luo, LiangShun, YanQing Su, JingJie Guo, XinZhong Li, and HengZhi Fu. "A simple model for lamellar peritectic coupled growth with peritectic reaction." Science in China Series G: Physics, Mechanics and Astronomy 50, no. 4 (August 2007): 442–50. http://dx.doi.org/10.1007/s11433-007-0042-x.

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17

Li, Yang, Jing Wang, Jiaquan Zhang, Changgui Cheng, and Zhi Zeng. "Deformation and Structure Difference of Steel Droplets during Initial Solidification." High Temperature Materials and Processes 36, no. 4 (April 1, 2017): 347–57. http://dx.doi.org/10.1515/htmp-2016-0113.

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AbstractThe surface quality of slabs is closely related with the initial solidification at very first seconds of molten steel near meniscus in mold during continuous casting. The solidification, structure, and free deformation for given steels have been investigated in droplet experiments by aid of Laser Scanning Confocal Microscope. It is observed that the appearances of solidified shells for high carbon steels and some hyper-peritectic steels with high carbon content show lamellar, while that for other steels show spherical. Convex is formed along the chilling direction for most steels, besides some occasions that concave is formed for high carbon steel at times. The deformation degree decreases gradually in order of hypo-peritectic steel, ultra-low carbon steel, hyper-peritectic steel, low carbon steel, and high carbon steel, which is consistent with the solidification shrinkage in macroscope during continuous casting. Additionally, the microstructure of solidified shell of hypo-peritectic steel is bainite, while that of hyper-peritectic steel is martensite.

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18

Terborg, R., and G. J. Schmitz. "Modeling of Peritectic YBa2Cu3O7−x Growth Using Transparent Organic Analogues." Journal of Materials Research 12, no. 8 (August 1997): 2002–8. http://dx.doi.org/10.1557/jmr.1997.0269.

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Transparent organic analogues were directionally solidified to investigate, via in situ observation the peritectic reaction occurring in the YBa2Cu3O7−x (YBCO)-superconductor system. Nucleation and growth of peritectic and properitectic phases were examined with respect to similarities with the solidification of the YBCO superconductor. The selected organic system, salicylic acid-acetamide, turned out to match the requirements concerning crystal shape, small nucleation rate of the peritectic phase on the properitectic phase, existence of stoichiometric phases with no solubility limits, and undercooling ability of the peritectic phase. Several features of YBCO growth which were previously deduced only from metallographic cross sections could be verified by direct observation. The organic analogue system will also be used in the future to improve numerical simulations.

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19

Kerr, H. W., and W. Kurz. "Solidification of peritectic alloys." International Materials Reviews 41, no. 4 (January 1996): 129–64. http://dx.doi.org/10.1179/imr.1996.41.4.129.

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20

Kwon, Young Soon, Pyuck Pa Choi, Ji Soon Kim, Dae Hwan Kwon, and K. B. Gerasimov. "Investigation of the Particle Size Effect on the Peritectic Melting of FeSn₂ Particles in FeSn₂-FeSn Nanocomposites." Solid State Phenomena 118 (December 2006): 651–54. http://dx.doi.org/10.4028/www.scientific.net/ssp.118.651.

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The particle size effect on the peritectic melting of FeSn2 particles in FeSn-FeSn2 nanocomposites was studied using differential scanning calorimetry and X-ray diffraction. FeSn-10 wt.% FeSn2 compounds, mechanically milled for 30 min and slowly heated in a differential scanning calorimeter, showed incongruent melting at 680 K. Although FeSn2 grains grew from 10 to 40 nm upon heating before peritectic melting set in, the melting temperature was more than 100 K lower than the equilibrium value. A small latent heat during peritectic melting and a large amount of interfacial energy of FeSn-FeSn2 nanocomposites are held responsible for this large particle size effect. Grain growth is hardly possible in the case of rapid local heating during mechanical milling. Therefore, a decrease in the peritectic melting temperature is even expected to be substantially larger.

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21

Guo, Junli, and Guanghua Wen. "Influence of Alloy Elements on Cracking in the Steel Ingot during Its Solidification." Metals 9, no. 8 (July 27, 2019): 836. http://dx.doi.org/10.3390/met9080836.

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The average steepness of |dT/d(fs)1/2| on the T − (fs)1/2 curve were calculated during peritectic solidification, which was used to investigate the effect of alloying elements on surface longitudinal cracks of peritectic steels in the solidification process. The value of |dT/d(fs)1/2| indicates the liquid feeding capacity between interdendrites during solidification, where cracks can easily occur if there is poor capacity of liquid feeding, as in peritectic solidification shrinkage. The cracking tendency as a function of carbon content was well described by the |dT/d(fs)1/2| at the cooling rates of 0.5, 5, and 10 °C/s, and the influences of other solute elements on |dT/d(fs)1/2| were also calculated. The results indicate that the possibility of crack occurrence increased and the maximum average steepness |dT/d(fs)1/2| changed from 496.75 °C located near 0.09C wt.% to 622.14 °C near 0.11C wt.% with increasing cooling rate. The value of |dT/d(fs)1/2| on the T − (fs)1/2 curve during the peritectic solidification can be used to analyze the solidification crack for peritectic steels.

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22

Peniel, Matthieu, Houda El Bekkachi, Olivier Tougait, Mathieu Pasturel, and Henri Noël. "An Experimental Investigation of the U-Mo-C Ternary Diagram." Solid State Phenomena 194 (November 2012): 26–30. http://dx.doi.org/10.4028/www.scientific.net/ssp.194.26.

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The isothermal sections of the U-Mo-C ternary system have been established at 1000°C and 1400°C, using powder X-ray diffraction, scanning electron microscopy coupled with energy dispersive X-ray analysis for the quantification of U and Mo and differential thermal analysis. The main differences between the two sections are the appearance of liquid phase at about 1230°C, due to the peritectic decomposition of γ-UMo, and the peritectoid decompositions of MoC and β’’ Mo2C. No other transformation was detected in this temperature range, especially one involving the two only ternary phases found, UMoC2 and U2Mo2C3.

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23

Xia, Qiong-Xia, Peng Gao, Guang Yang, Yong-Fei Zheng, Zi-Fu Zhao, Wan-Cai Li, and Xu Luo. "The Origin of Garnets in Anatectic Rocks from the Eastern Himalayan Syntaxis, Southeastern Tibet: Constraints from Major and Trace Element Zoning and Phase Equilibrium Relationships." Journal of Petrology 60, no. 11 (November 1, 2019): 2241–80. http://dx.doi.org/10.1093/petrology/egaa009.

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Abstract Amphibolite- and granulite-facies metamorphic rocks are common in the eastern Himalayan syntaxis of southeastern Tibet. These rocks are composed mainly of gneiss, amphibolite and schist that underwent various degrees of migmatization to produce leucogranites, pegmatites and felsic veins. Zircon U–Pb dating of biotite gneiss, leucocratic vein and vein granite from the syntaxis yields consistent ages of ∼49 Ma, indicating crustal anatexis during continental collision between India and Asia. Garnets in these rocks are categorized into peritecitc and anatectic varieties based on their mode of occurrence, mineral inclusions and major- and trace-element zoning. The peritectic garnets mainly occur in the biotite gneiss (mesosome layer) and leucocratic veins. They are anhedral and contain abundant mineral inclusions such as high-Ti biotites and quartz, and show almost homogeneous major-element compositions (except Ca) and decreasing HREE contents from core to rim, indicating growth during the P- and T-increasing anatexis. Peak anatectic conditions at 760–800°C and 9–10·5 kbar are well constrained by phase equilibrium calculations, mineral assemblages, and garnet isopleths. In contrast, anatectic garnets only occur in the vein granite. They are round or subhedral, contain quartz inclusions, and exhibit increasing spessartine and trace-element contents from core to rim. The garnet–biotite geothermometry and the garnet–biotite–plagioclase–quartz geobarometry suggest that the anatectic garnets crystallized at ∼620–650°C and 4–5 kbar. Some garnet grains show two-stage zoning in major and trace elements, with the core similar to the peritectic garnet but the rim similar to the anatectic garnet. Mineralogy, whole-rock major- and trace-element compositions and zircon O isotopes indicate that the two types of leucosomes were produced by hydration (water-present) melting and dehydration (water-absent) melting, respectively. The leucocratic veins contain peritectic garnet but no K-feldspar, have lower whole-rock K2O contents and Rb/Sr ratios, higher whole-rock CaO contents and Sr/Ba ratios, and show homogeneous δ18O values that are lower than those of relict zircons, indicating that such veins were produced by the hydration melting. In contrast, the vein granite contains peritectic garnet and K-feldspar, has higher whole-rock K2O contents and Rb/Sr ratios, lower whole-rock CaO contents and Sr/Ba ratios, and shows comparable δ18O values with those of relict zircons, suggesting that this granite were generated by the dehydration melting. Accordingly, both hydration and dehydration melting mechanisms have occurred in the eastern Himalayan syntaxis.

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24

Sun, Hong Liang, Cai Sun, Ze Wen Huang, and De Gui Zhu. "Peritectic Reaction of High Nb and W Pentatomic TiAl-Based Alloy." Advanced Materials Research 335-336 (September 2011): 831–35. http://dx.doi.org/10.4028/www.scientific.net/amr.335-336.831.

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The effect of different aluminum content on peritectic reaction and mechanical properties of pentatomic TiAl-based alloy was investigated. The results indicate that the grain size gradually increase with increasing content of aluminum and addition 45.7% aluminum in TiAl-based alloy results in that the peritectic reaction can increase grain size greatly, respectively. The content of aluminum can increase the room temperature strength, high temperature strength but peritectic reaction can effectively reduce tensile strength. Aluminum content has a little effect on the ductility. The stress rupture life has positive correlation relationship with the content of aluminum.

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25

Peng, Peng, Anqiao Zhang, Jinmian Yue, Shengyuan Li, Wanchao Zheng, and Li Lu. "Investigation on peritectic solidification in Sn-Ni peritectic alloys through in-situ observation." Journal of Materials Science & Technology 90 (November 2021): 236–42. http://dx.doi.org/10.1016/j.jmst.2021.01.094.

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26

Phelan, Dominic. "Influence of Undercooling on the Kinetics of the Peritectic Transition in an Fe-4.2wt%Ni Alloy." Materials Science Forum 649 (May 2010): 143–47. http://dx.doi.org/10.4028/www.scientific.net/msf.649.143.

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In-situ Laser Scanning Confocal Microscopy observations are presented that assess the influence of undercooling before the initiation of the peritectic transition in a Fe-4.2wt%Ni alloy on the resulting kinetics of the peritectic reaction and transformation. In a series of experiments varying the cooling rate, increasing the cooling rate led to a lower temperature at the L/ interface. The resulting peritectic reaction changed from slow 840m/s - 1500m/s, with limited growth into the  to rapid ~11mm/s with significant growth into . In continuous cooling experiments when the nucleation temperature was low, growth into  was high and the reacting species was observed to propagate along the liquid/delta-ferrite interface at a rate of ~11mm/s. The peritectic reaction rate did not appear to be a function of temperature over a measured nucleation temperature range of 5 K. Conversely, the growth rate of austenite into the delta-ferrite in the first 0.03 seconds was observed to increase from 1.5mm/s to 8mm/s as the measured temperature at nucleation decreased.

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27

Hu, Xiao Wu, Shuang Ming Li, Si Feng Gao, Lin Liu, and Heng Zhi Fu. "Microstructure Formation at Low Velocity during Directional Solidification of Pb-Bi Peritectic Alloys." Advanced Materials Research 97-101 (March 2010): 971–74. http://dx.doi.org/10.4028/www.scientific.net/amr.97-101.971.

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Directional solidification experiments on Pb-Bi peritectic alloys have been conducted at very low velocity (V=0.5 μm/s) and high thermal gradient (G=25 K/mm). Incomplete banded and oscillatory structures have been observed in both of hypoperitectic and hyperperitectic compositions over several millimeters of growth. These structures resulted from the repeated nucleation and competition between properitectic α- and peritectic β-phases. The banded or oscillatory structures are found to be transient and the final steady-state phase was only the peritectic β-phases. With an increase in composition, β phase formed and α phase disappeared at a lower solidified distance. Composition variations in the banded structure are measured to determine the solute distribution along the growth direction.

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28

Hillert, Mats, and Lars Höglund. "Melting of a peritectic phase." Scripta Materialia 50, no. 7 (April 2004): 1055–59. http://dx.doi.org/10.1016/j.scriptamat.2003.12.026.

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29

Takada, Jun, Hitoshi Kitaguchi, Akiyoshi Osaka, Yoshinari Miura, Katsuaki Takahashi, Mikio Takano, Yasunori Ikeda, et al. "Ba2YCu3OxCrystal Formed by Peritectic Reaction." Japanese Journal of Applied Physics 26, Part 2, No. 10 (October 20, 1987): L1707—L1710. http://dx.doi.org/10.1143/jjap.26.l1707.

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30

Akamatsu, Silvère, and Mathis Plapp. "Eutectic and peritectic solidification patterns." Current Opinion in Solid State and Materials Science 20, no. 1 (February 2016): 46–54. http://dx.doi.org/10.1016/j.cossms.2015.10.002.

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31

Boussinot, G., C. Hüter, R. Spatschek, and E. A. Brener. "Isothermal solidification in peritectic systems." Acta Materialia 75 (August 2014): 212–18. http://dx.doi.org/10.1016/j.actamat.2014.04.055.

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32

Moiseeva, L. A. "Peritectic crystallization of silicon steels." Metal Science and Heat Treatment 41, no. 5 (May 1999): 198–201. http://dx.doi.org/10.1007/bf02468419.

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33

XU, JIANG, YIDE KAN, and WENJIN LIU. "IN-SITU SYNTHETIC TiB2 PARTICULATE REINFORCED METAL MATRIX COMPOSITE COATING ON AA2024 ALUMINUM ALLOY BY LASER CLADDING TECHNOLOGY." Surface Review and Letters 12, no. 04 (August 2005): 561–67. http://dx.doi.org/10.1142/s0218625x05007438.

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In order to improve the wear resistance of aluminum alloy, in-situ synthesized TiB 2 and Ti 3 B 4 peritectic composite particulate reinforced metal matrix composite, formed on a 2024 aluminum alloy by laser cladding with a powder mixture of Fe -coated Boron, Ti and Al , was successfully achieved using 3-KW CW CO 2 laser. The chemical composition, microstructure and phase structure of the composite clad coating were analyzed by energy dispersive X-ray spectroscopy (EDX), SEM, AFM and XRD. The typical microstructure of the composite coating is composed of TiB 2, Ti 3 B 4, Al 3 Ti , Al 3 Fe and α- Al . The surface hardness of cladding coating increases with the amount of added Fe -coated B and Ti powder which determines the amount of TiB 2 and Ti 3 B 4 peritectic composite particulate. The nanohardness and the elastic modulus at the interface of the TiB 2 and Ti 3 B 4 peritectic composite particulate/matrix were investigated using the nanoindentation technique. The results showed that the nanohardness and the reduced elastic modulus from the peritectic composite particulate to the matrix is a gradient distribution.

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34

Sukhova, E. V. "The effect of carbon content and cooling rate on the structure of boron-rich Fe–B–C alloys." Physics and Chemistry of Solid State 21, no. 2 (June 15, 2020): 355–60. http://dx.doi.org/10.15330/pcss.21.2.355-360.

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The structural and phase composition of boron-rich Fe–В–С alloys in the concentration range of 9.0–16.0 % В, 0.001–1.7 % С, Fe – the balance (in wt. %) was investigated in this work. The cooling rate of the alloys was from 10 to 103 К/s. The methods of quantitative metallographic, X-ray, energy dispersive X-ray, and differential thermal analyses were applied. It was established that the maximal solubility of carbon in Fe2B hemiboride does not exceed 0.55 %, and that in FeB monoboride – 0.41 %. The alloys that belong to two-phase peritectic (Fe2(B,C)+Fe(B,C)) region, two-phase peritectic-eutectic (Fe2(B,C)+Fe(B,C)) region, and three-phase peritectic-eutectic (Fe2(B,C)+Fe(B,C)+C) region of the Fe–В–С phase diagram were distinguished depending on their structure. The appearance of an eutectic constituents in the investigated alloys was explained by transition of peritectic reaction L+Fe(В,С)®Fe2(В,С) to eutectic reaction L®Fe(В,С)+Fe2(В,С) within the temperature range of 1623–1583 К in the presence of carbon. With cooling rate increasing from 10 to 103 К/s, structural constituents tended to be fine, their volume fraction changed, microhardness and fracture toughness increased.

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35

Xu, Yiku, Zhaohao Huang, Yongnan Chen, Junxia Xiao, Jianmin Hao, Xianghui Hou, and Lin Liu. "Investigation of Microstructure Evolution and Phase Selection of Peritectic Cuce Alloy During High-Temperature Gradient Directional Solidification." Materials 13, no. 4 (February 19, 2020): 911. http://dx.doi.org/10.3390/ma13040911.

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In this work, a CuCe alloy was prepared using a directional solidification method at a series of withdrawal rates of 100, 25, 10, 8, and 5 μm/s. We found that the primary phase microstructure transforms from cellular crystals to cellular peritectic coupled growth and eventually, changes into dendrites as the withdrawal rate increases. The phase constituents in the directionally solidified samples were confirmed to be Cu2Ce, CuCe, and CuCe + Ce eutectics. The primary dendrite spacing was significantly refined with an increasing withdrawal rate, resulting in higher compressive strength and strain. Moreover, the cellular peritectic coupled growth at 10 μm/s further strengthened the alloy, with its compressive property reaching the maximum value of 266 MPa. Directional solidification was proven to be an impactful method to enhance the mechanical properties and produce well-aligned in situ composites in peritectic systems.

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Igarashi, K., H. Ohtani, and J. Mochinaga. "Phase Diagram of the System LaCl3-CaCl2-NaCl." Zeitschrift für Naturforschung A 42, no. 12 (December 1, 1987): 1421–24. http://dx.doi.org/10.1515/zna-1987-1212.

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The phase diagram of ternary system LaCl3-CaCl2-NaCl has been constructed from the phase diagrams of the three binary systems and of thirteen quasi-binary systems determined by DTA. For the binaries LaCl3-CaCl2 and CaCl2-NaCl eutectic points were observed at 651 °C , 35.1 mol% LaCl3 and at 508 °C , 49.9 mol% NaCl, respectively. For LaCl3-NaCl, a peritectic point besides the eutectic point at 545 °C , 36.1 mol% LaCl3 was found at 690 °C , 57.5 mol%, which is attributable to the formation of the peritectic compound 3 LaCl3 · NaCl. The phase diagram of the ternary system has a ternary eutetic point and a ternary peritectic point due to 3 LaCl3-NaCl, the form er at 462 °C and 12.1 - 3 9 .7 - 4 8 .2 mol% (LaCl3-CaCl2-NaCl) and the latter at 612 °C and 26.9 - 55.1 - 18.0 mol%.

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Wang, Shujie, Liangshun Luo, Yanqing Su, Fuyu Dong, Jingjie Guo, and Hengzhi Fu. "Two-phase separated growth and peritectic reaction during directional solidification of Cu–Ge peritectic alloys." Journal of Materials Research 28, no. 10 (April 24, 2013): 1372–77. http://dx.doi.org/10.1557/jmr.2013.93.

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38

Su, Y. Q., L. S. Luo, J. J. Guo, X. Z. Li, and H. Z. Fu. "Spacing selection of cellular peritectic coupled growth during directional solidification of Fe–Ni peritectic alloys." Journal of Alloys and Compounds 474, no. 1-2 (April 2009): L14—L17. http://dx.doi.org/10.1016/j.jallcom.2008.06.060.

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39

Zhang, S., M. J. M. Krane, and David R. Johnson. "Effects of Geometric Constraint on Solidification Microstructural Development of Peritectic TiAl Alloys." Materials Science Forum 783-786 (May 2014): 1147–52. http://dx.doi.org/10.4028/www.scientific.net/msf.783-786.1147.

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Directional solidification of binary peritectic TiAl alloys through preforms with straight channels with spacing on the order of the dendritic tip radius were simulated using a modified solid-liquid interface tracking model. Interruption of the steady-state growth of the primary β-phase by constraint of solutal diffusion within very thin sections of ceramic preforms can lead to solidification conditions favorable for the nucleation and continued growth of the peritectic α-phase even after the growth front has exited the preform.

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40

Chubukov, Mikhail Y., Dmitriy V. Rutskiy, and Dmitriy P. Uskov. "Analyzing the Features of Non-Metallic Inclusion Distribution in Ø410 mm Continuously Cast Billets of Low Carbon Steel Grades." Materials Science Forum 973 (November 2019): 21–25. http://dx.doi.org/10.4028/www.scientific.net/msf.973.21.

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The paper reports findings on the morphology of non-metallic inclusions in low carbon pre-peritectic and peritectic steel grades used for the fabrication of seamless pipes. It is demonstrated that the distribution of non-metallic inclusions over the cross section area of continuously cast billets is of a step-like nature conditioned by the features of billet solidification. In all the steels analyzed the non-metallic inclusions are presented by oxides, sulfides and complex oxi-sulfides not larger than 2 μm.

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41

Kim, Chan-Joong, Hee-Gyoun Lee, Ki-Baik Kim, and Gye-Won Hong. "Origin of the Y2Ba1Cu1O5 free region in melt-textured Y–Ba–Cu–O oxides." Journal of Materials Research 10, no. 9 (September 1995): 2235–40. http://dx.doi.org/10.1557/jmr.1995.2235.

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In order to understand the formation mechanism of the Y2BaCuO5 free region, microstructures concerning incongraent mehing and peritectic reaction were studied in melt-textured Y–Ba–Cu–O oxides. It is found that spherical pores form during incongruent melting of the YBa2Cu3O7−y phase into Y2BaCuO3 and a Ba–Cu–O liquid phase. As the melting goes on, liquid phase flows into the pores and then produces spherical liquid pockets containing a few Y2BaCuO5 particles. During slow cooling of the sample from the peritectic temperature to the temperature where YBa2Cu3O7−y phase is formed, the liquid pockets are converted into YBa2Cu3O7−y phase containing a few Y2BaCuO5 particles. Sometimes, remnant Ba–Cu–O liquid phase is present at the center part of the Y2BaCuO5 free regions due to the incomplete peritectic reaction. It is concluded that formation of spherical pores during incongruent melting of YBa2Cu3O7−y is responsible for the formation of the Y2BaCuO5 free regions.

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42

Takada, Jun, Hitoshi Kitaguchi, Akiyoshi Osaka, Yoshinari Miura, Katsuaki Takahashi, Yasunori Ikeda, Mikio Takano, et al. "Formation of YBa2Cu3Ox by peritectic reaction." Journal of the Japan Society of Powder and Powder Metallurgy 34, no. 10 (1987): 583–89. http://dx.doi.org/10.2497/jjspm.34.583.

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Sumida, Masaki, and Wilfried Kurz. "Peritectic equilibrium in Fe–Co alloys." Zeitschrift für Metallkunde 93, no. 11 (November 2002): 1154–56. http://dx.doi.org/10.3139/146.021154.

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Das, A., I. Manna, and S. K. Pabi. "A numerical model of peritectic transformation." Acta Materialia 47, no. 4 (March 1999): 1379–88. http://dx.doi.org/10.1016/s1359-6454(98)00427-3.

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Castanho, M. A. P., P. R. Goulart, C. Brito, J. E. Spinelli, N. Cheung, and A. Garcia. "Steady and unsteady state peritectic solidification." Materials Science and Technology 31, no. 1 (July 25, 2014): 105–14. http://dx.doi.org/10.1179/1743284714y.0000000616.

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46

Extremera, A. "The magnetic behaviour of NaHg4 peritectic." Physica Status Solidi (a) 105, no. 1 (January 16, 1988): 281–84. http://dx.doi.org/10.1002/pssa.2211050130.

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47

Kuklev, A. V., A. V. Leites, A. Yu Manuilov, and Yu M. Aizin. "Protection of peritectic steel in molds." Steel in Translation 37, no. 12 (December 2007): 1010–13. http://dx.doi.org/10.3103/s0967091207120108.

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48

Cao, Chongde, Xiaoyu Lu, and Bingbo Wei. "Peritectic solidification under high undercooling conditions." Chinese Science Bulletin 44, no. 14 (July 1999): 1338–43. http://dx.doi.org/10.1007/bf02885858.

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49

Boettinger, W. J., D. E. Newbury, N. W. M. Ritchie, M. E. Williams, U. R. Kattner, E. A. Lass, K. W. Moon, M. B. Katz, and J. H. Perepezko. "Solidification of Ni-Re Peritectic Alloys." Metallurgical and Materials Transactions A 50, no. 2 (November 27, 2018): 772–88. http://dx.doi.org/10.1007/s11661-018-5019-z.

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Adkins, N. J. E., N. Saunders, and P. Tsakiropoulos. "Rapid solidification of peritectic aluminium alloys." Materials Science and Engineering 98 (February 1988): 217–19. http://dx.doi.org/10.1016/0025-5416(88)90158-9.

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