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Acta Metall Sin  2018, Vol. 54 Issue (5): 809-823    DOI: 10.11900/0412.1961.2017.00559
Special Issue for the Solidification of Metallic Materials Current Issue | Archive | Adv Search |
Growth Behavior of Primary Intermetallic Phases and Mechanical Properties for Directionally Solidified Al-Mn-Be Alloy
Huijun KANG1, Jinling LI1, Tongmin WANG1(), Jingjie GUO2
1 Key Laboratory of Solidification Control and Digital Preparation Technology (Liaoning Province), School of Materials Science and Engineering, Dalian University of Technology, Dalian 116024, China
2 National Key Laboratory for Precision Hot Processing of Metals, Harbin Institute of Technology, Harbin 150001, China
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Abstract  

Intermetallic compounds (including quasicrystals) have been widely employed as reinforced phases in many alloys due to their high strength, high hardness and good thermal stability. The growth behavior and growth pattern of these intermetallic compounds affect the mechanical properties of materials significantly. However, the intermetallic compound, which exhibits complex crystal structures and directional bonding usually shows a faceted growth pattern with strong anisotropy and forms crystals with a wide range of morphologies and coarse grains during solidification. The inappropriate morphology and size of the intermetallic compound will destroy the integrity of the matrix and thus deteriorate the mechanical properties of materials. In this work, the microstructural evolution, morphology evolution of intermetallic compounds and mechanical properties have been investigated in directionally solidified Al-3Mn-7Be (atomic fraction, %) alloy with a wide pulling rates of 1~1500 μm/s. The addition of Be results in the shift of Al-Mn binary phase diagram toward the Mn-rich side, the appearance of intermetallic compounds, namely λ-phase, T-phase, Be4AlMn, and icosahedral quasicrystal (I-phase) and significantly refines the microstructures of the as-cast and directionally solidified samples. With increasing pulling rates, a transition of primary phase is observed from λ-phase to T-phase, and then I-phase, accompanied by the formation of the primary Be4AlMn phase, which can be attributed to the increase of supersaturation and supercooling near the solid/liquid interface. Meanwhile, the morphology, size and growth pattern of primary phases vary with the increase of pulling rates. The mechanical properties of directionally solidified Al-3Mn-7Be alloy have been investigated. It is indicated that the room-temperature strength of this alloy decreases first and then increases as the pulling rates increase, and a larger elongation is presented at the lowest and highest pulling rates, which can be attributed to the microstructures of alloys, properties of strengthening phases and the interfaces between matrix and strengthening phase.

Key words:  Al-Mn-Be alloy      directional solidification      intermetallic compound      microstructure      3D morphology      mechanical property     
Received:  27 December 2017     
ZTFLH:  TG111.4  
Fund: Supported by National Natural Science Foundation of China (Nos.51774065, 51525401, 51690163 and 51601028)

Cite this article: 

Huijun KANG, Jinling LI, Tongmin WANG, Jingjie GUO. Growth Behavior of Primary Intermetallic Phases and Mechanical Properties for Directionally Solidified Al-Mn-Be Alloy. Acta Metall Sin, 2018, 54(5): 809-823.

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https://www.ams.org.cn/EN/10.11900/0412.1961.2017.00559     OR     https://www.ams.org.cn/EN/Y2018/V54/I5/809

Fig.1  XRD spectra (a) and microstructures of as-cast Al-3Mn (b) and Al-3Mn-7Be (c) alloys, AES analyses of phases composition (d) and DSC curve (e) of as-cast Al-3Mn-7Be alloy
Fig.2  Microstructures of the longitudinal section of directionally solidified Al-3Mn-7Be alloy at pulling rates of 1 μm/s (a), 5 μm/s (b), 60 μm/s (c), 600 μm/s (d) and 1000 μm/s (e) (Insets are corresponding SAED patterns of primary phases)
Fig.3  3D morphologies of λ-phase obtained at a pulling rate of 1 μm/s
(a) regular hexagonal prisms along longitudinal direction
(b) regular hexagonal prisms along cross section direction
(c) irregular prisms along cross section direction
Fig.4  Projections of λ-phase unit cell along the [0001] (a) and [1010] (b) directions, respectively
Fig.5  3D morphologies of T-phase at different pulling rates
(a) 5 μm/s (b) 90 μm/s (c) 200 μm/s, along [0001] direction (d) 200 μm/s, along [1120] direction (e) 400 μm/s (f) 600 μm/s
Fig.6  Bright field TEM image of the Be4AlMn and T-phase (a), composite SAED pattern of Be4AlMn and T-phase (b), and SAED patterns of Be4AlMn (c) and T-phase (d)
Fig.7  Octahedral (a) and spinel twin (b) morphologies of Be4AlMn (Insets sketch the formation of a typical spinel twinned crystal, and the twin plane is shaded. bbb indicates the (111) twin plane)
Fig.8  Room-temperature tensile stress-strain curves of directional solidified Al-3Mn-7Be alloys at different pulling rates and corresponding microstructures (insets)
Pulling rate /(μms-1) UTS / MPa YS / MPa Elongation / % Elastic modulus / GPa
0 78 71 2.99 66.5
1 184 116 15.62 94.6
5 146 88 6.33 41.9
60 189 103 9.48 67.1
200 215 115 9.65 77.3
1000 244 123 12.01 64.4
Table 1  Room-temperature tensile properties of directional solidified Al-3Mn-7Be alloys at different pulling rates
Fig.9  Microstructures of deformational zone of directional solidified Al-3Mn-7Be alloys near fracture surface at pulling rates of 60 μm/s (a), 400 μm/s (b) and 1000 μm/s (c)
Fig.10  TEM analyses of directionally solidified Al-3Mn-7Be alloy at a pulling rate of 1000 mm/s
(a) bright-field image
(b, c) SEAD patterns of I-phase and α-Al in Fig.10a
(d) HRTEM image of the interface between I-phase and α-Al
(e, f) Fouier transform of regions "1" and "2" in Fig.10d
Fig.11  Bright field TEM image of the directionally solidified Al-3Mn-7Be alloy at a pulling rate of 1000 μm/s after tensile test at room temperature (High-density dislocations are observed and the dislocation lines terminating at I-phase particles)
Fig.12  Fractographs of as-cast and directional solidified Al-3Mn-7Be alloys at different pulling rates (Insets show the magnified images corresponding to the squares)
(a) as-cast (b) 1 μm/s (c) 5 μm/s (d) 60 μm/s (e) 200 μm/s (f) 1000 μm/s
[1] Shechtman D, Blech I, Gratias D, et al.Metallic phase with long-range orientational order and no translational symmetry[J]. Phys. Rev. Lett., 1984, 53: 1951
[2] Hargittai I.Dan Shechtman's quasicrystal discovery in perspective[J]. Israel J. Chem., 2011, 51: 1144
[3] Lubensky T C, Ramaswamy S, Toner J, et al.Dislocation motion in quasicrystals and implications for macroscopic properties[J]. Phys. Rev., 1986, 33B: 7715
[4] Watanabe M, Inoue A, Kimura H M.High mechanical strength of rapidly solidified Al92Mn6Ln2 (Ln=lanthanide metal) alloys with finely mixed icosahedral and Al phases[J]. Mater. Trans. JIM, 1993, 34: 162
[5] Bae D H, Kim S H, Kim D H, et al.Deformation behavior of Mg-Zn-Y alloys reinforced by icosahedral quasicrystalline particles[J]. Acta Mater., 2002, 50: 2343
[6] Bae D H, Lee M H, Kim K T, et al.Application of quasicrystalline particles as a strengthening phase in Mg-Zn-Y alloys[J]. J. Alloys Compd., 2002, 342: 445
[7] Park E S, Yi S, Ok J B, et al. Solidification and microstructure control of Mg-rich alloys in the Mg-Zn-Y ternary systemya [J]. MRS Online Proc. Libr. Arch., 2000, 643: K2.5
[8] Singh A, Nakamura M, Watanabe M, et al.Quasicrystal strengthened Mg-Zn-Y alloys by extrusion[J]. Scr. Mater., 2003, 49: 417
[9] Singh A, Osawa Y, Somekawa H, et al.Ultra-fine grain size and isotropic very high strength by direct extrusion of chill-cast Mg-Zn-Y alloys containing quasicrystal phase[J]. Scr. Mater., 2011, 64: 661
[10] Goel D B, Roorkee U P, Furrer P, et al.Precipitation in aluminum manganese (iron, copper) alloys[J]. Aluminium, 1974, 50: 511
[11] Huang K, Zhang K, Marthinsen K, et al.Controlling grain structure and texture in Al-Mn from the competition between precipitation and recrystallization[J]. Acta Mater., 2017, 141: 360
[12] Kang H J, Li X Z, Su Y Q, et al.3-D morphology and growth mechanism of primary Al6Mn intermetallic compound in directionally solidified Al-3at.%Mn alloy[J]. Intermetallics, 2012, 23: 32
[13] Song G S, Fleury E, Kim S H, et al.Enhancement of the quasicrystal-forming ability in Al-based alloys by Be-addition[J]. J. Alloys Compd., 2002, 342: 251
[14] Chang H J, Fleury E, Song G S, et al. Formation of quasicrystalline phases in Al-rich Al-Mn-Be alloys [J]. J. Non-Cryst. Solids, 2004, 334-335: 12
[15] Zupani? F, Bon?ina T, Kri?man A, et al.Quasicrystalline phase in melt-spun Al-Mn-Be ribbons[J]. J. Alloys Compd., 2008, 452: 343
[16] Zupani? F, Markoli B, Nagli? I, et al.Phases in the Al-corner of the Al-Mn-Be System[J]. Microsc. Microanal., 2013, 19: 1308
[17] Liu G H, Zhang Y, Li X Z, et al.Thermal stabilization treatment and the effect on the microstructure in directionally solidified Ti-52%Al alloy[J]. Acta Metall. Sin., 2014, 50: 329(刘国怀, 张元, 李新中等. 定向凝固Ti-52%Al合金热稳定处理及其对微观组织的影响[J]. 金属学报, 2014, 50: 329)
[18] Luo L S, Liu T, Zhang Y N, et al.Microstructure evolution and growth behoviors of faceted phase in directionally solidified Al-Y alloys I. Microstructure evolution of directionally solidified Al-15%Y hypereutectic alloy[J]. Acta Metall. Sin., 2016, 52: 859(骆良顺, 刘桐, 张延宁等, 定向凝固Al-Y合金组织演化规律及小平面相生长I. Al-15%Y过共晶合金组织演化规律[J]. 金属学报, 2016, 52: 859)
[19] Kang H J, Wang T M, Lu Y P, et al.Controllable 3D morphology and growth mechanism of quasicrystalline phase in directionally solidified Al-Mn-Be alloy[J]. J. Mater. Res., 2014, 29: 2547
[20] Zupani? F, Bon?ina T, ?u?tar?i? B, et al.Microstructure of Al-Mn-Be melt-spun ribbons[J]. Mater. Charact., 2008, 59: 1245
[21] Jansson ?.A thermodynamic evaluation of the Al-Mn system[J]. Metall. Trans., 1992, 23A: 2953
[22] Raynor G V, Faulkner C R, Noden J D, et al.Ternary alloys formed by aluminium, transitional metals and divalent metals[J]. Acta Metall., 1953, 1: 629
[23] Kim S H, Song G S, Fleury E, et al.Icosahedral quasicrystalline and hexagonal approximant phases in the Al-Mn-Be alloy system[J]. Philos. Mag., 2002, 82A: 1495
[24] Kreiner G, Franzen H F.The crystal structure of λ-Al4Mn[J]. J. Alloys Compd., 1997, 261: 83
[25] Kelly P M, Ren H P, Qiu D, et al.Identifying close-packed planes in complex crystal structures[J]. Acta Mater., 2010, 58: 3091
[26] Robinson K.The structure of β(AlMnSi)-Mn3SiAl9[J]. Acta Cryst., 1952, 5: 397
[27] Kurz W, Fisher D J, translated by Li J G, Hu Q D. Fundamentals of Solidification [M]. Beijing: Higher Education Press, 2010: 59(Kurz W,Fisher D J著, 李建国, 胡侨丹译. 凝固原理 [M]. 北京: 高等教育出版社, 2010: 59)
[28] B?gels G, Buijnsters J G, Verhaegen S A C, et al. Morphology and growth mechanism of multiply twinned AgBr and AgCl needle crystals[J]. J. Cryst. Growth, 1999, 203: 554
[29] Fleury E, Chang H J, Kim D H.Heterogeneous nucleation of icosahedral phase from FCC phase in cast Al87Mn4Si2Be7 alloy[J]. Philos. Mag., 2006, 86: 349
[30] Carrabine J A.Ternary AlMnBe4 phases in commercially pure beryllium[J]. J. Nucl. Mater., 1963, 8: 278
[31] Li C, Wu Y Y, Li H, et al.Morphological evolution and growth mechanism of primary Mg2Si phase in Al-Mg2Si alloys[J]. Acta Mater., 2011, 59: 1058
[32] Hamilton D R, Seidensticker R G.Propagation mechanism of germanium dendrites[J]. J. Appl. Phys., 1960, 31: 1165
[33] Kang H J.Growth behaviour of primary-crystalline phases and mechanical properties of directionally solidified Al-Mn-(Be) alloys [D]. Harbin: Harbin Institute of Technology, 2013(康慧君. 定向凝固Al-Mn-(Be)合金先结晶相生长行为及力学性能 [D]. 哈尔滨: 哈尔滨工业大学, 2013)
[34] Singh A, Watanabe M, Kato A, et al.Microstructure and strength of quasicrystal containing extruded Mg-Zn-Y alloys for elevated temperature application[J]. Mater. Sci. Eng., 2004, A385: 382
[35] Lloyd D J.Particle reinforced aluminium and magnesium matrix composites[J]. Int. Mater. Rev., 1994, 39: 1
[36] Kang H J, Wu S P, Li X Z, et al.Improvement of microstructure and mechanical properties of Mg-8Gd-3Y by adding Mg3Zn6Y icosahedral phase alloy[J]. Mater. Sci. Eng. 2011, A528: 5585
[37] Zhang K Y, Bigot J, Chevalier J P, et al.Dodecahedral-shaped quasicrystalline precipitates in dilute Al-Mn solid solutions[J]. Philos. Mag., 1988, 58B: 1
[38] Ohashi T, Dai L, Fukatsu N, et al.Precipitation of quasicrystalline phase in rapidly solidified Al-Mn-Zr alloys[J]. Scr. Metall., 1986, 20: 1241
[39] Loiseau A, Lapasset G.Relations between quasicrystals and crystalline phases in Al-Li-Cu-Mg alloys: A new class of approximant structures[J]. Philos. Mag. Lett., 1987, 56: 165
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