Zr元素对Al-Mn-Si-Zn系铝合金组织与性能的影响

Trans. Nonferrous Met. Soc. China 24(2014) 3872?

3878

Effect of Zr addition on microstructure and

properties of Al?Mn?Si?Zn-based alloy

Jun-chao ZHANG, Dong-yan DING, Wen-long ZHANG1, Shao-hai KANG1,

Xing-long XU1, Yong-jin GAO2, Guo-zhen CHEN2, Wei-gao CHEN2, Xiao-hua YOU2 1.School of Materials Science and Engineering, Shanghai Jiao Tong University, Shanghai 200240, China;

2. Huafon Nikki Al Co., Ltd., Shanghai 201506, China

Received 17 October 2013; accepted 5 November 2014

11Abstract: Effects of Zr addition on the microstructure, mechanical and electrochemical properties of Al?Mn?Si?Zn alloy were investigated. Transmission electron microscopy (TEM) observations reveal that, in as-annealled state, the precipitates in the Zr-containing alloy are finer and more dispersive than those in the Zr-free alloy. Whereas, in simulated brazing state, a weaker precipitation is found in the Zr-containing alloy. Tensile testing results indicate that, with Zr additon, comprehensive mechanical properties of the as-annealed alloys could be significantly improved but weakened for the simulated brazing alloy. Electrochemical testing results reveal that, with Zr addition, the corrosion resistance of the as-annealed alloy decreases. However, after the simulated brazing treatment, such a negative effect of Zr element on the corrosion behavior of the alloy could be negligible.

Key words: aluminium alloy; Zr alloying; precipitation; corrosion; mechanical property

lower temperature like 500 °C, such a phase

transformation will take a longer annealing time more 1 Introduction

than 120 h [13]. For Al?0.18%Zr alloys metastable Al3Zr

Zr is one of the important alloying elements to phase could not transform to equilibrium Al3Zr phase improve the microstructures and properties of aluminum even after 700 h of annealing at 460 °C. However, alloys. When Zr is added to aluminum alloys, Zr element equilibrium Al3Zr phase could directly form from the may exist in four kinds of forms at different heat solid solution cooled down at certain situations (higher processing and heat-treatment stages, i.e., solid solution temperature) [14]. Large quantity of equilibrium η-Al3Zr in matrix, coarse primary Al3Zr phase, metastable Al3Zr phase particles could form in the Al?0.5%Zr alloy which

was slowly cooled down from the annealling temperature phase as well as equilibrium Al3Zr phase. If the amount

of 600 °C [15,16]. The migration of large angle grain of Zr addition is too high, coarse primary Al3Zr dendritic

boundaries often resulted in the change of phases will form and aggravate the mechanical properties

crystallography relationship between Al3Zr particles and of the Al alloys [1]. The metastable Al3Zr phase is

usually much finer and coherent with the matrix with a the matrix from coherent or half-coherent to incoherent mismatch ratio of only 0.8%. It is a kind of very effective state [2].

strengthening dispersoid, which can inhibit Zr addition to Al?Zn?Mg or Al?Cu alloys could recrystallization, refine the microstructure and increase result in inhibited recrystallization, increased the recrystallization temperature and strength of the recrystallization temperature, improved strength and matrix alloys [2?7]. Whereas, the equilibrium Al3Zr fracture property as well as anti-corrosion behavior of

the alloys. SUN et al [17] found that Zr addition could phase is usually coarse and incoherent with the

lead to the formation of homogeneously distributed matrix [8?12].

It was reported that metastable Al3Zr phase in skeleton-like non-eutectic phase (Al2CuMg+AlZnMgCu) Al?0.5% Zr alloy could transform to equilibrium Al3Zr and secondary precipitates. LI et al [16] found that Zr

element preferred to refine the as-cast and recrystallized phase after several hours of annealing at 640 °C. At a

Foundation item: Proejct (51171108) supported by the National Natural Science Foundation of China; Project supported by Shanghai High-tech

Development Project, China

Corresponding author: Dong-yan DING; Tel: +86-21-34202741; E-mail: dyding@http://wendang.chazidian.com

DOI: 10.1016/S1003-6326(14)63545-7

Jun-chao ZHANG, et al/Trans. Nonferrous Met. Soc. China 24(2014) 3872?3878 3873

microstructures. And the strength, hardness and elongation of the alloys increased with increase of the Zr content. When the Zr content was over 0.19%, coarse Al3Zr phase formed in the as-cast microstructure and the mechanical properties of the alloys were aggravated. And for 2159Al alloy, the appropriate Zr content was 0.19% [1]. An intergranular corrosion which is near the grain boundaries is a relatively common corrosion form [18]. If the alloy happens in this form of corrosion, the alloy strength may drop dramatically, which often causes a catastrophic consequence. ZHANG et al [19] reported that the anti-intergranular corrosion property of 7055Al alloys could be improved with increase of the Zr content from 0 to 0.15% .

To date, few literatures have been reported on the effect of Zr addition on Al?Mn-based alloys although Zr element has been used to enhance the brazing properties of modified 3003Al alloys. Therefore, in the present work, the effect of Zr content on the microstructure and properties of an Al?Mn?Si?Fe?Zn alloy was studied, which has been developed for heat-exchange applications. This comprehensive investigation should help for a better understanding of the role of Zr element in affecting the annealing and heat-treatment microstructures, mechanical properties and corrosion behaviors.

2 Experimental

The chemical composition of the aluminum alloys is

shown in Table 1. All of the alloys contained the same

contents of Mn, Si, Fe and Zn elements but different

content of Zr element. Corresponding alloy foils with a

thickness of 0.1 mm were produced through the same

processes, i.e., casting and hot rolling as well as cold

rolling. After a finish rolling, some alloy foils were

annealed at 400 °C for 2 h. And other alloy foils were

heat-treated at 600 °C for 5 min in a furnace and then

quickly cooled down to room temperature, which is a

simulation of the brazing process.

Table 1 Chemical composition of alloys (mass fraction, %)

Alloy Mn Si Fe Zr ZnAl

Zr-free 1.2 1.1 0.5 0 1.5Bal.

Zr-containing 1.2 1.1 0.5 0.2 1.5Bal.

Microstructures of the heat-treated alloys were characterized with JEM?2100F transmission electron microscope (TEM). The TEM specimens were prepared

through electrolytic polishing in 4% HClO4 and methanol solutions, followed by an ion beam thinning. Tensile testings were carried out on Zwick universal

tensile machine. The tensile rate was 1 mm/min. Five tensile samples were used for obtaining the average values of mechanical properties. The tensile fracture surfaces of the alloys were examined with a field emmision scanning electron microscope (SEM, FEI SIRION 200).

Specimens for the electrochemical experiments were degreased with acetone and rinsed in distilled water. Three parrallel specimens for each testing were used to confirm the experimental results. The electrochemical testing with 0.5% NaCl solution was carried out at room temperature. Tafel measurements were performed in a three-electrode system with a CHI660C interface. The specimen, saturated calomel electrode (SCE) and a platinum plate were used as the working electrode, reference electrode and counter electrode, respectively. The potential sweep rate was 1 mV/s. Before testing, the alloy sample was stabilized for 30 min in the electrolyte. All potentials were reported versus those of the SCE. The corrosion surfaces obtained after the electrochemical testings were also examined by SEM.

3 Results and discussion

3.1 Microstructure

Figure 1 shows TEM images of the precipitates in the as-annealed alloys. Although some micrometer-sized precipitates may be found in the alloys, the size of most of the precipitates in the Zr-free alloy usually varies from several tens of nanometers to 200 nm. These precipitates are found to be AlMnSi and AlMnFeSi phases according to the EDX analyses. And most of them have an ellipsoidal shape (see Fig. 1(a)). Compared with the Zr-free alloy, the Zr-containing alloy has a finer and denser precipitation (see Fig. 1(b)). It is obvious that the Zr addition to the alloy could refine and promote the precipitation of the alloy, resulting in uniformly distributed precipitates. However, the Zr-additon has no much effect on the morphology of the precipitates in the as-annealed alloy. Figure 2 shows TEM images of the simulated brazing alloys. In comparison with the precipitates in the

as-annealed alloys, the precipitates in the simulated

brazing alloys present quite different precipitation

densities and slight in different shapes. Although the size

of the precipitates is usually ranging from several tens of nanometers to 200 nm, the Zr-containing alloy has a lower precipation density than the Zr-free alloy, which is

quite different from the as-annealed alloys. This suggests that for the simulated brazing alloys, Zr addition mainly affects the density of the precipates in the alloys, but has little effect on the size and morphology of the precipates.

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Jun-chao ZHANG, et al/Trans. Nonferrous Met. Soc. China 24(2014) 3872?3878

Fig. 1 TEM micrographs of as-annealed alloys: (a) Zr-free alloy; (b) Zr-containing alloy

Fig. 2 TEM micrographs of simulated brazing alloys: (a) Zr-free alloy; (b) Zr-containing alloy

During the simulated brazing process (heating up to Table 2 Tensile testing results of alloys

600 °C), a large quntity of precipitates in the alloys will dissolve into α(Al) matrix since solid solubility of alloying elements in the simulated brazing alloy matrix is higher than that in the as-annealed alloy matrix at a lower temperature (400 °C). And during the subsequent air-cooling of the simulated brazing process, the cooling rate is relatively higher. Therefore, alloying elements may still super-saturate in the α(Al) matrix. Our experimental results indicate that the Zr addition could restrain the precipitation in the brazing process probably through promoting the dissolution of other alloying elements in the α(Al) matrix.

Alloy Heat-treatment

As-annealed

Zr-free

Simulated treatment As-annealed

Zr-containing

Simulated treatment

σs/MPa σb/MPaδ/%

13.4711.4415.9211.20

61.14 127.1455.63 145.8775.82 138.8751.87 142.10

alloy are 75.82 MPa, 138.87 MPa and 15.92%, respectively. It is remarkable that, with 0.2% Zr addition, the yield strength, tensile strength and elongation of the as-annealed alloy have increase of 24.01%, 9.23% and

18.12%, respectively. These facts reveal that the Zr 3.2 Mechanical properties

addition could lead to excellent comprehensive The tensile testing results of the two kinds of alloys

mechanical properties for the as-annealed alloys. are shown in Table 2. The yield strength, tensile strength

Table 2 also shows the mechanicla properties of the and elongation of the as-annealed Zr-free alloy are

61.14 MPa, 127.14 MPa and 13.47%, respectively. simulated brazing alloys. The yield strength, tensile

strength and elongation of the Zr-free alloy are 56.63 Corresponding values of the as-annealed Zr-containing

Jun-chao ZHANG, et al/Trans. Nonferrous Met. Soc. China 24(2014) 3872?3878 3875

MPa, 145.87 MPa and 11.44%, respectively. Compared with the Zr-free alloy, the yield strength, tensile strength and elongation of the Zr-containing alloy are slightly low. Obviously, mechanical enhancement through the 0.2% Zr addition does not occur for the simulated brazing alloys, which is quite different from the annealed alloys.

It is well known that several strengthening mechanisms such as solution strenthening, grain refining strenthening and precipitate strenthening may decide the mechanical performance of alumnium alloys [20]. Considering the TEM observations that Zr addition could lead to a stronger precipitation in the as-annealed state but a weakened precipitation in the brazing state, we believe that the above mechanical difference in the two kinds of alloys should be mainly caused by the difference in precipitate strengthening. As an important alloying element, Zr may contribute to the precipitation of ultrafine Al3Zr particles, which could be nucleation centers for primary or secondary precipitates. The experimental results on the annealed alloys reveal that finer and denser precipitates could form in the Zr-containing alloy rather than in the Zr-free alloy. Such a uniform and dense precipitation should be favorable for a precipitate strengthening and results in the enhanced mechanical properties. For the simulated brazing alloys the precipitation has been weakened after Zr addition, which is unfavorable for the precipitate strengthening. As a result, the strengthening effect through Zr addition does

not appear in the high-temperature heat-treated alloys.

SEM images of the tensile fracture surfaces of both as-annealed and simulated brazing alloys are shown in Figs. 3 and 4. All of the alloys show a ductile fracture with a large quantity of dimples on the fracture surface. Different dimple size and fracture at large precipitates could be observed. The relatively fine dimples on the fracture surfaces of the annealed Zr-containing alloy rather than the annealed Zr-free alloy seem to be a good explaination for the enhanced mechanical property (elongation) through Zr addition.

3.3 Electrochemical properties

Figure 5 presents the Tafel polarization curves of the studied alloys tested in 0.5% NaCl solution. Corresponding electrochemical parameters are listed in Table 3. As shown in Fig. 5(a), the anode branch of the Tafel polarization curve of the Zr-free alloy presents an active dissolution feature with its pitting potential (φpit) highly close to the corrosion potential (φcorr), which suggests that the Zr-free alloy should be sensitive to pitting corrosion. Compared with the Zr-free alloy, the φcorr of the Zr-containing alloy is ?877 mV, which is much lower than that (?763 mV) of the Zr-free alloy (see Table 3). With Zr addition to the alloy, both the cathode reaction and the anode reaction are enhanced. And the polarization curve moves to the high current density area, which indicates that the corrosion reaction of Al alloy is

Fig. 3 SEM images showing tensile fracture of as-annealed alloys: (a) Zr-free alloy; (b) Zr-containing alloy

Fig. 4 SEM images showing tensile fracture of simulated brazing alloys: (a) Zr-free alloy; (b) Zr-containing alloy

3876 Jun-chao ZHANG, et al/Trans. Nonferrous Met. Soc. China 24(2014) 3872?3878

Fig. 5 Tafel polarization curves of alloys: (a) As-annealed; (b) Simulated brazing

Table 3 Tafel polarization parameters of alloys tested in 0.5% NaCl solution Alloy

Heat- φcorr Jcorr/ Corrosion treatment (vs SCE)/mV (µA·cm?2

) form As-annealed

?763 34.05 Pitting Zr-free

Simulated

treatment ?718 35.07 Pitting Zr-

As-annealed

?877 124.3

Intergranular corrosioncontaining Simulated

treatment ?715 18.92 Pitting

enhanced. The corrosion current density of the Zr-free alloy is 34.05 µA/cm2, while the corrosion current density of the Zr-containing alloy is 124.3 µA/cm2 (see Table 3). This indicates that 0.2% Zr addition to the alloy will aggravate the corrosion resistance of the annealed alloy in the NaCl solution.

Figure 6 shows the corrosion surface of the annealed alloys tested in the NaCl solution. Many corrosion pits are visible on the surface of the Zr-free alloy (see Fig. 6(a)), which shows a pitting feature. Whereas, the corrosion characteristics of the

Zr-containing alloy belong to an evident intergranular corrosion. Obviously, 0.2% Zr addition to the alloy results in a great change of the corrosion behavior of the annealed alloy.

Fig. 6 Corrosion surface of annealed alloys tested in 0.5% NaCl solution: (a) Zr-free alloy; (b) Zr-containing alloy

Figure 5(b) also shows the Tafel polarization curves of the simulated brazing alloys tested in 0.5% NaCl solution. Polarization curves of the two kinds of alloys nearly coincide with each other. As shown in Table 3, the corrosion potentials of the Zr-free alloy and Zr-containing alloy are ?718 mV and ?715 mV, respectively. Unlike the intergranular corrosion for the annealed alloy, the simulated brazing Zr-containing alloy demonstrates a pitting corrosion (see Fig. 7), which is similar to that of the Zr-free alloy. This indicates that the adverse effect of Zr addition on the corrosion performance of the alloy could be greatly minimized after the brazing treatment.

According to the dilution theory for explanation of the intergranular corrosion mechanism of aluminium alloys, the difference of corrosion potential between grain boundary anode phase or precipitate free zone (PFZ) and matrix contributes to the galvanic corrosion and then evolutes intergranular corrosion. This theory considers that corrosion cells can form among grain boundary precipitates, PFZ and inter-grains when the Zr-free alloys are put in corrosion media. The grain boundary precipitates may be anode or cathode phase. While the PFZ tends to become anode and dissolves at the first stage, which provides rapid propagation path for the intergranular corrosion. Therefore, an intergranular