Characterisation of Mg–Li alloy processed by solution treatment and large strain rolling

Abstract

The effects of solution treatment and large strain rolling (LSR) on the microstructure and mechanical properties of Mg–10.73Li–4.49Al–0.52Y alloy were investigated. Results showed that after solution treatment, α-phase and AlLi phase were dissolved into β matrix, which led to the increase of strength. With the increased temperature of LSR, new phase MgLi₂Al (θ-phase) and AlLi phase precipitated from the matrix in turns. The Mg–Li alloy rolled at 623 K with 75 reduction showed the ultimate tensile strength of 328 MPa, which was more superior to many other Mg–Li alloys. The excellent strength could be explained by the mechanisms of solution strengthening and fine grain strengthening.

Keywords

Mg–Li alloy Solution treatment Large strain rolling

Introduction

Mg–Li alloy is one of the lightest structural metallic materials, which shows great potential in transportation systems and electric equipments due to the high specific strength and good formability at ambient temperature.^1,2 Furthermore, The addition of Li to magnesium alloy can not only reduce its density but also markedly improve the formability by changing the crystal structure from hexagonal close packed to body centred cubic (BCC) when the amount of Li exceeds 11 wt-.³ The β-phase Mg–Li alloy has lower density and better formability than other α-phase or (α+β)-phase alloys. However, with the increasing amount of Li, the Mg–Li alloy presents lower strength and poorer corrosion resistance, which limits its application. Ternary or quaternary β-phase Mg–Li alloy is designed to overcome these drawbacks. It has been demonstrated that with the addition of Al or Zn element, the tensile strength and hardness of Mg–Li–Al or Mg–Li–Zn ternary alloy increases significantly due to solution and precipitation strengthening.^4,5 However, the stability of these alloys is relatively poor, because the θ-phase (MgLi₂Al) or θ′-phase (MgLi₂Zn) is a metastable strengthening phase, which is liable to decompose to AlLi phase (a softening phase) during ambient or high temperature aging process.^6,7 Therefore, other elements, such as Ag,¹ Ca,⁸ Ce or other Re,^9–11 have been added to stabilise the mechanical properties of the alloys.

Besides microalloying of magnesium, various kinds of thermomechanical treatments, such as conventional rolling and extrusion^12,13 and severe plastic deformation (SPD), have been used to improve the strength of metallic materials by refining their microstructure. It is accepted that SPD is one of the most effective ways to fabricate materials with fine or ultrafine grains; however, most of the SPD technologies have complex process and are difficult to be applied in the industry. It is noteworthy that as one of the SPDs, large strain rolling (LSR) could obtain fine or ultrafine microstructure with inexpensive and simple methods. Pérez-Prado et al.¹⁴ reported AM60 alloy with the significant increasing ultimate strength of 378 MPa processed by LSR. Xu et al.¹⁵ studied the Mg–8.2Gd–3.8Y–1.0Zn–0.4Zr alloy after LSR with total reduction of 96. The microstructure was significantly refined and became much more homogeneous. The alloy exhibited excellent mechanical properties with ultimate strength of 403 MPa and elongation to failure of 13.7 at room temperature along the rolling direction (RD). However, there are few studies on the preparation of Mg–Li alloy by the LSR process.

In the present investigation, Y element is added in Mg–Li–Al alloy to improve the stability of mechanical properties. Then, solution treatment and LSR process with single pass reduction of 50 and total reduction of 75 are imposed on the as cast alloy. Last, the effects of both solution treatment and LSR process on the microstructure and mechanical properties of the alloy are investigated.

Experimental

The Mg–10.73Li–4.49Al–0.52Y alloy used in this experiment was prepared in a vacuum induction furnace at an atmosphere of pure argon. Plates with 50 mm in the RD, 30 mm in the transverse direction (TD) and 10 mm in the normal direction (ND) were cut directly from the as cast ingot and were solution treated at 623 K for 3.5 h and then quenched in water. To prevent oxidation, the plates were clad with aluminium foil and then covered with powdered graphite during solution treatment.

The LSR process of the solution treated plates was conducted for two passes with the temperature range from 473 to 623 K. The reduction in thickness of the plates was ∼50 for each pass, which resulted in a total reduction of 75. Before each passes, the plates were reheated for 10 min. The detailed LSR schedule was summarised in Table 1.

Table 1

LSR schedule for solution treated Mg–Li alloy

Material	Name	Rolling temperature/K	Actual reduction for 1st pass/	Actual reduction for 2nd pass/	Actual total reduction/
Mg–Li alloy (T4)	D1	473	48.2	49.4	73.8
	D2	523	49.7	48.4	74.1
	D3	573	51.0	47.6	74.3
	D4	623	49.9	50.0	74.9

Specimens for microstructural examination were cut in the ND-RD plane of the rolled plates and then etched with a solution of 4 vol.- nitric acid in alcohol. Microstructure observation was performed using a Leica DMI 5000 optical microscope. ASTM E112 standard was used to calculate the average grain size. A Phenom PROX scanning electron microscopy (SEM) equipped with energy dispersive spectrometer (EDS) was used to examine the distribution of element for the as cast and solution treated Mg–Li alloys. X-ray diffraction (XRD) measurement of the phases in the alloys conducted on TD-RD plane was detected by a Bruker D8 Advance diffractometer using Cu K_α X-ray tube operated at 40 kV voltages under a scanning speed of 0.2° s^− 1.

Tensile specimens with gauge length of 5 mm and cross-section of 3 × 2 mm² were cut from the samples of as cast and solution treated Mg–Li alloys and from the plates processed by LSR parallel to RD. Tensile test was performed on a SANSCMT 5105 universal testing machine with an initial strain rate of 2.0 × 10^− 3 s^− 1 at room temperature. The fracture morphology of specimens after tensile testing was observed by SEM (NOVA NANOSEM 430, FEI, USA).

Results

Microstructure of as cast and solution treated Mg–Li alloy

The microstructure of as cast and solution treated Mg–Li alloy is shown in Fig. 1. Previous study indicated that the experimental alloy is mainly made up of β-phase, while small fraction of α-phase disperses in the β-matrix and along the phase boundary.¹⁶ In addition, there are many precipitate phases of Al₂Y and AlLi dispersed in the grain. It can be seen from Fig. 1a that the β-phase presents equiaxed grains with the grain size between 300 and 1000 μm. As shown in Fig. 1b, no noticeable change in the grain size is observed in solution treated specimen, as compared with the as cast one. Figures 2 and 3 show the EDS elemental mapping (consisting of Mg, Al and Y distribution) and XRD spectrum respectively. It reveals that after solution treatment, both AlLi phase and α-phase (in the β-matrix and along the β-phase boundary) disappear and only Al₂Y phase remains, which demonstrates that both AlLi and α-phase have dissolved in the β-matrix.

Microstructure of a as cast and b solution treated Mg–Li alloys

Typical SEM image of a as cast and b solution treated Mg–Li alloys and elemental mapping of Mg, Al and Y by EDS

XRD patterns of as cast and solution treated Mg–Li alloys

Microstructure of LSRed Mg–Li alloy

Figure 4 shows the microstructure of Mg–Li alloys after second LSR at different temperatures. The Mg–Li alloy exhibits a typical fibrous rolling texture, in which β-phase and other precipitated phases are elongated approximately parallel to the RD (as shown with a black arrow in Fig. 4a). No obvious dynamic recrystallisation occurs during the LSR at 473–523 K, while some small recrystallised grains align in the RD at 573 K. As shown in Fig. 4e and f, a necklace-like structure containing fine dynamic recrystallisation grains ∼4.4 μm and coarse grains ∼126.4 μm in width is formed when the LSR temperature reaches 623 K. It is considered that the necklace-like structure is caused by the continuous dynamic recrystallisation (CDRX).^17–19 Generally, twin dynamic recrystallisation or low temperature dynamic recrystallisation is likely to occur in the Mg alloy with certain strain at 473 K or below due to the low stacking fault energy (SFE).²⁰ In the present study, however, the nucleation of DRX by twin formation is not revealed in LSR Mg–Li alloy at 473 K (Fig. 4a). Furthermore, no evidence of DRX associated with other mechanism can be seen when temperature reaches 523 K. It can be explained by the faster diffusion rate of β-phase and the higher SFE of BCC Mg–Li alloy, which will promote the dynamic recovery and hinder the formation of DRX nuclei.^21,22

Microstructure of a D1 treated, b D2 treated, c, d D3 treated, and e, f D4 treated Mg–Li alloys

Figure 5 shows the XRD spectra of Mg–Li alloy after the second pass LSR at 473–623 K. As can be seen, newly formed θ-phase (MgLi₂Al) precipitates from β-phase after LSR at 473–523 K, while AlLi phase precipitates at 573 K. However, there are no obvious changes when the temperature reaches 623 K. Figure 6 shows the XRD spectra of Mg–Li alloy after first and second pass LSR at 523 K. It can be seen that θ-phase precipitates from β-phase after the first pass, while θ-phase and AlLi phase coexist after the second pass. It is demonstrated that θ-phase is a metastable phase,¹ which is liable to be transferred to the AlLi phase during the preheating before the second pass LSR at 523 K.

XRD patterns of Mg–Li alloy after second LSR at 473–623 K

XRD patterns of Mg–Li alloy after LSR at 523 K

XRD patterns of β-phase in Mg–Li alloy after the second LSR at 473–623 K are shown in Fig. 7. Compared with Fig. 3, Fig. 7 shows that the Mg–Li alloy possesses strongest (200)_β peak intensity after the second LSR at 473–573 K. It is reported that cold rolled BCC metals tend to have {100}_β planes parallel to the rolling plane.⁶ This feature is conductive to plasticity parallel to the RD of the Mg–Li alloy. As seen in Fig. 7, the β-phase is transferred to have the strongest (110)_β peak intensity when the LSR temperature reaches 623 K. As mentioned above, significant CDRX takes place in the Mg–Li alloy during this process, which might be the reason for such change.

Indices of crystal faces of β-phase in Mg–Li alloy after second LSR at 473–623 K

Mechanical properties of Mg–Li alloy before and after LSR

Figure 8 shows the tensile stress–strain curves of Mg–Li alloy before and after the LSR process. The ultimate strength and elongation of as cast Mg–Li alloy are 131 MPa and 47.1 respectively. After solution treatment, the ultimate strength increased to 194 MPa and the elongation decreased to 1.2.

Engineering stress–strain curves of Mg–Li alloys with different processes tested along RD at ambient temperature

Carefully examining Fig. 3, it can be found that XRD peaks of β-phase have shifted slightly to higher 2θ after solution treatment. According to Fig. 3, the plane spacing d_hkl of the significant (hkl)_β X-ray peak is calculated for Mg–Li plates before and after solution treatment, and the result is shown in Table 2. As can be seen, the d_hkl value for each (hkl)_β peak decreases when the Mg–Li alloy is solution treated. The atomic radii of Mg and Al are 0.160 and 0.143 nm respectively.⁶ Thus, large amount of Al element is dissolved into the β-matrix after solution treatment, which would lead to the decrease of d_hkl value for (hkl)_β peaks and would result in the increase of interatomic bonding force and hinder the movement of dislocation. Such significant effect of solution strengthening leads to the obvious increase of strength and decrease of plasticity of solution treated Mg–Li alloy.

Table 2

2θ and d spacing of significant β-phase peaks of as cast and solution treated Mg–Li alloys

	As cast		Solution treated
β-Phase peak	2θ	d/Å	2θ	d/Å
(110)	35.994	2.4931	36.315	2.4718
(200)	51.822	1.7627	52.041	1.7559
(211)	64.735	1.4388	65.039	1.4329
(220)	76.380	1.2459	76.572	1.2432

As can be seen from Fig. 8, with the LSR temperature rising, the strength of Mg–Li alloy increases, which is the result of various effects of strengthening mechanism. Compared with solution treated Mg–Li alloy, the grain size of D1 and D2 samples decreases to some extent, which is favourable for the strength. In addition, the θ strengthening phase that precipitates from the β-phase can further improve the strength. Small recrystallised grains appear when the LSR temperature reaches 573–623 K, which significantly impedes the slide of the dislocation and improves the strength of the Mg–Li alloy. Furthermore, the phase composition of D4 sample is the same with the solution treated Mg–Li alloy, which means that the solution strengthening is the other important reason for the increase of strength.

The elongation of the Mg–Li alloy after LSR at 473–523 K increases significantly compared with the solution treated alloy, which is due to the existence of (200)_β texture paralleled to the RD plane. However, non-uniform microstructure caused by CDRX weakens the effect of rolling texture to the plasticity when the LSR temperature reaches 573 K. So, the elongation of D3 sample is only 7.8. The rolling texture is replaced by (110)_β recrystallisation texture after the LSR process at 623 K, resulting in the poorer elongation compared to the Mg–Li alloy by the LSR process at 473–573 K.

The mechanical properties tested at ambient temperature of D2 and D4 samples and other Mg–Li alloys are listed in Table 3. It can be seen that the Mg–Li alloys processed by the LSR exhibit superior strength and keep a certain plasticity.

Table 3

Summary of mechanical properties tested at room temperature of different Mg–Li alloys

Alloys	Condition	UTS/MPa	Elongation/
Mg–10.73Li–4.49Al–0.52Y	D2 (in the present paper)	223	24.3
Mg–10.73Li–4.49Al–0.52Y	D4 (in the present paper)	328	5.1
Mg–10.73Li–4.49Al–0.52Y (Ref. 23)	ECAP	166.4	53
Mg–5Li–3Al–1Sn–0.4Mn (Ref. 24)	Extruded	258	16.0
Mg–5.21Li–3.44Zn–0.32Y–0.01Zr (Ref. 25)	Extruded	215	21
Mg–5Li–3Al–2Zn–0.5RE (Ref. 26)	Extruded	294.1	26.6
Mg–8Li–1Al (Ref. 27)	Rolled (0.14 mm)	313.9	3.2
Mg–8Li–1Al–1Zn (Ref. 27)	Rolled (0.14 mm)	233.39	9.2
Mg–8Li–2Al–2RE (Ref. 28)	Cold rolled	202	37
LAZ1110 (Ref. 29)	T4+rolling	276	20
Mg–14.3Li–0.8Zn (Ref. 2)	T4+rolling	227	33

Figure 9 shows SEM images of the tensile fracture surfaces for the Mg–Li alloys before and after LSR. Figure 9a is the image of as cast specimen. The fracture surface is mainly composed of large dimples and a small quantity of cleavage planes. After solution treatment, typical characteristics of brittle fracture with large river pattern can be seen from the fracture surface of the specimen (Fig. 9b). The SEM images of D2 specimen in Fig. 9c and d show a ductile fracture surface, in which a large number of deep dimples can be observed. When the temperature of the LSR process reaches 623 K, as shown in Fig. 9e and f, the fracture surface of D4 specimen is composed of many large cleavage planes except small dimples, indicating that the brittle fracture is the primary characteristics of the alloy but ductile characteristics still exist.

Fractured surfaces of a as cast, b solution treated, c, d D2 treated, and e, f D4 treated Mg–Li alloy

Conclusions

The microstructure and mechanical properties of Mg–10.73Li–4.49Al–0.52Y alloy processed by solution treatment and LSR have been investigated. The following conclusions could be drawn from this study: (i)

The as cast Mg–Li alloy was composed of β-phase, α-phase, Al₂Y phase and AlLi phase. After solution treatment, the Al₂Y phase and AlLi phase were dissolved into the β-matrix, while no significant change could be seen from the grain size.

(ii)

With the increase of deformation temperature, the θ-phase and AlLi precipitated from the β-matrix.

(iii)

All the specimens exhibited a typical fibrous rolling texture with (200)_β texture paralleled to the RD plane after LSR at 473–573 K. When the deformation temperature reached 623 K, typical necklace-like microstructure appeared due to the effect of CDRX, and the rolling texture was replaced by (110)_β recrystallisation texture.

(iv)

Owing to the effects of solution strengthening and fine grain strengthening, the UTS of the Mg–Li alloy after rolling at 623 K with 75 reduction significantly increased to 328 MPa.

Footnotes

Acknowledgement

This work was supported by the Guangzhou Science and Technology Development Program [grant no. 2009Z2-D811].

References

R. Z.

and Zhang

M. L.

: ‘Microstructure, mechanical properties and aging behavior of Mg-5Li-3Al-2Zn-xAg’, Mater. Sci. Eng. A, 2009, A520, 36–39. doi: 10.1016/j.msea.2009.05.008

Gzyl

, PesciIn

, Rosochowski

, Boczkal

and Olejnik

: ‘In situ analysis of the influence of twinning on the strain hardening rate and fracture mechanism in AZ31B magnesium alloy’, J. Mater. Sci., 2015, 50, 2532–2543. doi: 10.1007/s10853-014-8812-0

Nayeb-Hashemi

A. A.

, Clark

J. B.

and Pelton

A. D.

: ‘The Li–Mg (lithium–magnesium) system. Bull: alloy phase diagrams’, 365–374; 1984, New York, Springer.

Wei

X. W.

, Zu

X. T.

and Zhou

W. L.

: ‘Compressive creep behaviour of Mg–Li–Al alloy’, Mater. Sci. Technol., 2006, 22, 730–733. doi: 10.1179/174328406X86083

Liu

F. C.

, Tan

M. J.

, Liao

, Ma

Z. Y.

, Meng

and Nakata

: ‘Microstructural evolution and superplastic behavior in friction stir processed Mg–Li–Al–Zn alloy’, J. Mater. Sci., 2013, 48, 8539–8546. doi: 10.1007/s10853-013-7672-3

S. K.

, Li

Y. H.

, Chien

K. T.

, Chien

and Yang

C. S.

: ‘X-ray diffraction studies on cold-rolled/solid–solution treated α+β Mg–10.2Li–1.2Al–0.4Zn alloy’, J. Alloys Compd, 2013, 563, 234–241. doi: 10.1016/j.jallcom.2013.02.073

Gutiérrez-Urrutia

: ‘Study of isothermal δ’ (Al3Li) precipitation in an Al–Li alloy by thermoelectric power’, J. Mater. Sci., 2011, 46, 3144–3150. doi: 10.1007/s10853-010-5195-8

Jiang

, Zhang

C. H.

, Wang

, Qu

Z. K.

, Wu

R. Z.

and Zhang

M. L.

: ‘Creep behaviors of Mg–5Li–3Al–(0,1)Ca alloys’, Mater. Des., 2012, 34, 863–866. doi: 10.1016/j.matdes.2011.08.023

L. B.

, Cui

C. L.

, Wu

R. Z.

, Li

J. Q.

, Zhan

H. B.

and Zhang

M. L.

: ‘Effects of Ce-rich RE additions and heat treatment on the microstructure and tensile properties of Mg–Li–Al–Zn-based alloy’, Mater. Sci. Eng. A, 2011, A528, 2174–2179. doi: 10.1016/j.msea.2010.11.063

10.

Cui

C. L.

, Wu

L. B.

, Wu

R. Z.

, Zhang

J. H.

and Zhang

M. L.

: ‘Influence of yttrium on microstructure and mechanical properties of as-cast Mg–5Li–3Al–2Zn alloy’, J. Alloys Compd, 2011, 509, 9045–9049. doi: 10.1016/j.jallcom.2011.04.030

11.

Wang

, Zhang

M. L.

, Niu

Z. Y.

and Liu

: ‘Influence of rare earth elements on microstructure and mechanical properties of Mg–Li alloys’, J. Rare Earth, 2006, 24, 797–800. doi: 10.1016/S1002-0721(07)60032-5

12.

Luo

, Xia

, Wang

H. Y.

, Chen

, Wang

J. G.

and Jiang

Q. C.

: ‘Microstructure and tensile properties of new type of hot rolled Mg–3Sn–1Zn alloy sheet at elevated temperatures’, Mater. Sci. Technol., 2014, 30, 1305–1308. doi: 10.1179/1743284714Y.0000000565

13.

Zhu

T. L.

, Sun

J. F.

, Cui

C. L.

, Wu

R. Z.

, Betsofen

, Leng

, Zhang

J. H.

and Zhang

M. L.

: ‘Influence of Y and Nd on microstructure, texture and anisotropy of Mg–5Li–1Al alloy’, Mater. Sci. Eng. A, 2014, A600, 1–7.

14.

Pérez-Prado

M. T.

, Del Valle

J. A.

and Ruano

O. A.

: ‘Achieving high strength in commercial Mg cast alloys through large strain rolling’, Mater. Lett., 2005, 59, 3299–3303. doi: 10.1016/j.matlet.2005.04.061

15.

, Xu

S. W.

, Zheng

M. Y.

, Wu

, Wang

E. D.

, Kamado

, Wang

G. J.

and Lv

X. Y.

: ‘Microstructures and mechanical properties of high-strength Mg–Gd–Y–Zn–Zr alloy sheets processed by severe hot rolling’, J. Alloys Compd, 2012, 524, 46–52. doi: 10.1016/j.jallcom.2012.02.050

16.

Lin

, Kang

Z. X.

, Fang

and Zhang

J. Y.

: ‘Microstructure and mechanical properties of Mg–Li alloy processed by severe plastic deformation and annealing’, Chin. J. Nonferrous Met., 2013, 23, 3267–3274.

17.

Galiyev

, Kaibyshev

and Sakai

: ‘Continuous dynamic recrystallization in magnesium alloy’, Mater. Sci. Forum, 2003, 419–422, 509–514. doi: 10.4028/https-www-scientific-net-443.webvpn1.xju.edu.cn/MSF.419-422.509

18.

Barnett

M. R.

: ‘Influence of deformation conditions and texture on the high temperature flow stress of magnesium AZ31’, J. Light Met., 2001, 1, 167–177. doi: 10.1016/S1471-5317(01)00010-4

19.

, Liu

, Gan

, Tan

and Wang

: ‘Modified twinning behaviour induced by texture evolution in hot rolled Mg–3Al–1Zn alloy’, Mater. Sci. Technol., 2014, 30, 694–699. doi: 10.1179/1743284713Y.0000000404

20.

Zhao

Z. Y.

, Guan

R. G.

, Wang

, Dai

C. G.

, An

C. G.

, Liu

C. M.

and Lee

C. S.

: ‘Effects of dynamic recrystallisation during deep rolling of semisolid slab and heat treatment on microstructure and properties of AZ31 alloy’, Mater. Sci. Technol., 2014, 30, 309–315. doi: 10.1179/1743284713Y.0000000343

21.

Sivakesavam

and Prasad

Y. V. R. K.

: ‘Characteristics of superplasticity domain in the processing map for hot working of as-cast Mg–11.5Li–1.5Al alloy’, Mater. Sci. Eng. A, 2002, A323, 270–277. doi: 10.1016/S0921-5093(01)01392-2

22.

Cao

F. R.

, Ding

, Li

Y. L.

and Zhou

: ‘Superplasticity, microstructural evolution and deformation mechanism of super-light two-phase Mg–Li alloys’, Chin. J. Nonferrous Met., 2009, 19, 1908–1916. doi: 10.1016/S1003-6326(08)60301-5

23.

Kong

, Liu

and Kang

Z. X.

: ‘Microstructure and mechanical properties of two-phase Mg–10.73Li–4.49Al–0.52Y alloy processed by ECAP’, Chin. J. Nonferrous Met., 2012, 22, 2415–2423. doi: 10.1016/S1003-6326(11)61147-3

24.

Kim

Y. H.

, Kim

J. H.

, Yu

H. S.

, Choi

J. W.

and Son

H. T.

: ‘Microstructure and mechanical properties of Mg–xLi–3Al–1Sn–0.4Mn alloys (x = 5, 8 and 11 wt-)’, J. Alloys Compd, 2014, 583, 15–20. doi: 10.1016/j.jallcom.2013.08.154

25.

Chen

Z. Y.

, Dong

Z. C.

, Yu

and Tong

: ‘Microstructure and properties of Mg–5.21Li–3.44Zn–0.32Y–0.01Zr alloy’, Mater. Sci. Eng. A, 2013, A559, 651–654. doi: 10.1016/j.msea.2012.09.005

26.

Z. K.

, Wu

L. B.

, Wu

R. Z.

, Zhang

J. H.

, Zhang

M. L.

and Liu

: ‘Microstructures and tensile properties of hot extruded Mg–5Li–3Al–2Zn–xRE (Rare Earths) alloys’, Mater. Des., 2014, 54, 792–795. doi: 10.1016/j.matdes.2013.08.077

27.

Meng

X. R.

, Wu

R. Z.

, Zhang

M. L.

, Wu

L. B.

and Cui

C. L.

: ‘Microstructures and properties of superlight Mg–Li–Al–Zn wrought alloys’, J. Alloys Compd, 2009, 486, 722–725. doi: 10.1016/j.jallcom.2009.07.047

28.

Yan

, Chen

R. S.

and Han

E. H.

: ‘Microstructures and mechanical properties of cold rolled Mg–8Li and Mg–8Li–2Al–2RE alloys’, Trans. Nonferrous Met. Soc. China, 2010, 20, s550–s554. doi: 10.1016/S1003-6326(10)60536-5

29.

Wang

J. Y.

: ‘Mechanical properties of room temperature rolled MgLiAlZn alloy’, J. Alloys Compd, 2009, 485, 241–244. doi: 10.1016/j.jallcom.2009.06.047