Joint effect of quasicrystalline icosahedral and L12-strucutred phases precipitation on the grain structure and mechanical properties of aluminum-based alloys

doi:10.1016/j.jmst.2021.01.055

Abstract

Abstract:

Dispersoid hardening is a key factor in increasing the recrystallization resistance and mechanical strength of non-heat treatable aluminum-based alloys. Mn and Zr are the main elements that form dispersoids in commercial Al-based alloys. In this work, the annealing-induced precipitation behavior, the grain structure, and the mechanical properties of Al-3.0Mg-1.1 Mn and Al-3.0Mg-1.1 Mn-0.25 Zr alloys were studied. The microstructure and the mechanical properties were significantly affected by annealing regimes after casting for both alloys. The research demonstrated a possibility to form high-density distributed quasicrystalline-structured I-phase precipitates with a mean size of 29 nm during low-temperature annealing of as-cast alloys. Fine manganese-bearing precipitates of I-phase increased recrystallization resistance and significantly enhanced the mechanical strength of the alloys studied. The estimated strengthening effect owing to I-phase precipitation was 150 MPa. Due to the formation of L1₂-structured Al₃Zr dispersoids with a mean size of 5.7 nm, additional alloying with Zr increased yield strength by about 90 MPa. The L1₂-phase strengthening effect was estimated through the dislocation bypass looping and shearing mechanisms.

Key words: Aluminum alloy, Quasicrystals, Dispersoid hardening, Recrystallization, Mechanical properties

A.G. Mochugovskiy, N. Yu. Tabachkova, M. Esmaeili Ghayoumabadi, V.V. Cheverikin, A.V. Mikhaylovskaya. Joint effect of quasicrystalline icosahedral and L1₂-strucutred phases precipitation on the grain structure and mechanical properties of aluminum-based alloys[J]. J. Mater. Sci. Technol., 2021, 87: 196-206.

Figures/Tables 11

Fig. 1. (a-e, g-k) SEM and (f, l) TEM microstructures of the as-cast (a-f) Al-Mg-Mn and (g-l) Al-Mg-Mn-Zr alloys; (b-e) and (h-k) are the elemental distribution SEM-EDS maps for Al, Mg, Mn, and Zr; inserts in (f) and (l) are corresponding SAEDs.

Fig. 2. Hardness dependences on the time of the first annealing step for one-step (solid lines) and two-step (dotted lines) regimes for the (a) Al-Mg-Mn and (b) Al-Mg-Mn-Zr alloys.

Fig. 3. TEM images of the Al-Mg-Mn alloys annealed (a-c) at 350 °C for 8 h, (d-f) in two steps at 350 °C for 4 h and at 400 °C for 4 h, and (g-i) at 450 °C for 8 h; (a, d, g) bright-field images, (b, e, h) dark-field images, and (c, f, i) the corresponding SAEDs; the green cycles mark up the reflexes of the dark field images.

Fig. 4. TEM images of the Al-Mg-Mn-Zr (a-c) alloy annealed at 350 °C for 16 h (d-f), 48 h (g-h), and at 450 °C for 8 h (g-i); bright-field images (a, d, g), dark-field images (b, e, h), and the corresponding SAEDs (c, f, i); the green cycles mark up the reflexes of the dark field images.

Fig. 5. TEM images of the Al-Mg-Mn-Zr alloy annealed in two steps at 350 °C for 32 h and at 400 °C for 4 h; bright-field images (a, d), dark-field images (b, e), and the corresponding SAEDs (c, f); the green cycles mark up the reflexes of the dark field images.

Fig. 6. TEM-EDS spectrums corresponding to the I-phase in the Al-Mg-Mn alloy annealed at 350 °C for 48 h (a) and the Al-Mg-Mn-Zr alloy annealed at 350 °C for 32 h and at 400 °C for 4 h (b); the spectrum 1 and 2 areas are shown in Figs. 3(d) and 4(d), respectively.

Fig. 7. High-resolution TEM-structures of the (a) Al-Mn-Mg and (b-d) Al-Mn-Mg-Zr alloys after annealing at 350 °C for (a, b) 16 h and (c, d) 48 h; (d) shows the high-magnified image marked up in (c) by blue dotted area; the inserts are FFT corresponding to the precipitate areas.

Fig. 8. TEM images of the thermomechanical-treated samples for the (a, d) Al-Mg-Mn alloy and (b, c, e, f) Al-Mg-Mn-Zr alloy pre-annealed in two steps; (a-c) bright-field images, (d-f) dark-field images (b, e), insert in (f) is corresponding SAED; the green cycle mark up the reflex for the dark field image.

Fig. 9. Grain structures of the (a-d) Al-Mg-Mn and (e-h) Al-Mg-Mn-Zr alloys after 30 min annealing at 400 °C for the samples pre-annealed (homogenized) at (a, e) 350 °C, 8 h; (b, f) 350 °C, 48 h, (c) 350 °C, 4 h + 400 °C, 4 h, (g) 350 °C, 32 h + 400 °C, 4 h, and (d, h) 450 °C, 8 h (OM, polarized light).

Fig. 10. EBSD-maps and the corresponding grain boundary misorientation angle distributions for the (a) Al-Mg-Mn and (b-d) Al-Mg-Mn-Zr alloys after 30 min of post-deformation annealing at 400 °C for the samples pre-annealed (after casting) at (a, b) 350 °C for 8 h, (c) 350 °C for 32 h + 400 °C for 4 h, and (d) 450 °C for 8 h; rolling direction is horizontal.

Table 1 Mechanical properties of the thermomechanical-treated Al-Mg-Mn and Al-Mg-Mn-Zr alloys pre-annealed for various regimes.

Pre-annealing regime	Precipitates type	Post-deformation annealing of cold-rolled sheet at 250 °C (non-recrystallized grain structure)			Post-deformation annealing of cold-rolled sheet at 400 °C
Pre-annealing regime	Precipitates type	YS (MPa)	UTS (MPa)	El (%)	YS (MPa)	UTS (MPa)	El (%)	Dominated grain structure *
Al-3.0Mg-1.1 Mn
350 °C/8 h	I	314 ± 6	364 ± 8	8 ± 2	222 ± 7	316 ± 5	17 ± 2	NR
350 °C/16 h	I	318 ± 4	370 ± 6	10 ± 3	230 ± 4	330 ± 2	16 ± 1	NR
350 °C/48 h	I; (Al,Mn)	318 ± 2	373 ± 2	11 ± 2	243 ± 4	340 ± 2	17 ± 2	NR
350 °C/4 h + 400 °C /4 h	I; (Al,Mn)	316 ± 6	372 ± 6	11 ± 2	229 ± 5	327 ± 4	16 ± 2	NR
450 °C/8 h	Al₆Mn	278 ± 4	339 ± 4	10 ± 2	124 ± 4	278 ± 5	24 ± 2	R
Al-3.0Mg-1.1 Mn-0.25 Zr alloy
350 °C/8 h	I	319 ± 6	369 ± 6	7 ± 2	254 ± 3	344 ± 3	14 ± 3	NR
350 °C/16 h	I	322 ± 6	372 ± 5	8 ± 1	253 ± 3	342 ± 4	14 ± 1	NR
350 °C/48 h	I; (Al,Mn) L1₂	345 ± 4	391 ± 2	8 ± 1	263 ± 3	353 ± 3	15 ± 2	NR
350 °C/32 h + 400 °C /4 h	I; (Al,Mn) L1₂	361 ± 2	402 ± 5	9 ± 1	274 ± 4	360 ± 3	14 ± 1	NR
450 °C/8 h	I; (Al,Mn) L1₂;Al₆Mn	321 ± 5	375 ± 4	11 ± 2	145 ± 7	292 ± 6	23 ± 2	R
350 °C/16 h (Al-3Mg)	-	169 ± 2	232 ± 3	18 ± 1
360 °C/32 h + 400 °C/4 h (Al-3Mg-0.25 Zr [62])	L1₂	240 ± 3	300 ± 2	19 ± 1
36 0 °C/4 h + 400 °C/4 h (Al-3Mg-0.2Zr-0.1Sc [63])	L1₂	230 ± 5	295 ± 6	12 ± 1

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Joint effect of quasicrystalline icosahedral and L1₂-strucutred phases precipitation on the grain structure and mechanical properties of aluminum-based alloys

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