Effect of Al on Microstructure and Properties of Hot-Rolled 2205 Dual Stainless Steel

Meng, Qian; La, Peiqing; Yao, Liang; Zhang, Peng; Wei, Yupeng; Guo, Xin

doi:https://doi.org/10.1155/2016/7518067

Advances in Materials Science and Engineering

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Research Article | Open Access

Volume 2016 | Article ID 7518067 | https://doi.org/10.1155/2016/7518067

Effect of Al on Microstructure and Properties of Hot-Rolled 2205 Dual Stainless Steel

Qian Meng,^1,2Peiqing La ,¹Liang Yao,¹Peng Zhang,¹Yupeng Wei,¹and Xin Guo¹

Academic Editor: Ming-Xing Zhang

Received15 Feb 2016

Revised18 May 2016

Accepted07 Jun 2016

Published05 Jul 2016

Abstract

The microstructure, mechanical properties, oxidation, and corrosion resistance of 2205 stainless steels without and with Al in a range of 0.5 to 2.5 wt.% were investigated in this paper. The results showed that the matrix phase transformed from austenite to ferrite. The volume fraction of the ferrite in the steels decreased at first and then increased and was the lowest in the steel with 0.5 wt.% Al. Most of the Al was dissolved in the ferrite and austenite phases in the steels. The ultimate tensile strength and elongation rate of the steels increased at first and then decreased with the increasing Al content, with the highest values in the steel with 0.5 wt.% Al. The yield strength of the steels slightly increased from 544 to 607 MPa due to the addition of Al. The oxidation rates of the steels with Al were much lower than that of the steel without Al, and the rate of the steel with 1.5 wt.% Al was the lowest, approximately 10 times lower than that of the steel without Al. The corrosion rates of the steels with 0.5 and 1.0 wt.% Al were slightly higher than that of the alloy without Al. In general, the steel with 1 wt.% Al had optimal properties.

1. Introduction

2205 stainless steel has received extensive attention due to its superior mechanical properties and good corrosion resistance in Cl⁻ environments [1–4]. The Cr₂O₃ protective scale formed on the steel surface plays a key factor in determining the corrosion and oxidation resistance, but it is substantially damaged by water vapour due to the formation of volatile Cr oxyhydroxide species when the steel is exposed to a certain range of high temperature for a long time [5–7].

Al₂O₃ scale shows greater thermodynamic stability in oxygen than Cr₂O₃ and offers superior protection in many industrially relevant environments [8–10]. Yamamoto et al. reported that the Al₂O₃ scale can maintain good resistance to oxidation in air with 10% water vapour at 650 and 800°C for Fe-20Ni-14Cr-2.4Al steel [11]. A number of works over the past 40 years have created Al₂O₃-forming austenite stainless steels [12–16], but studies on Al₂O₃-forming 2205 stainless steel have not yet been reported. Al is a strong ferrite stabilizer, so the addition of Al to 2205 stainless steel may change the phase balance of austenite and ferrite, which may change the mechanical and corrosion resistance of the alloys. A key need is the concurrent development of strength and corrosion resistance.

In our previous works, 316L and 310S steels with different Al contents were fabricated by vacuum induction melting, and good corrosion and oxidation resistance were obtained with no loss of strength [17–20].

In this paper, the effects of the Al content on the microstructure, mechanical properties, corrosion, and oxidation resistance of 2205 stainless steel were investigated to develop a new microstructure- and property-tailoring method and develop a new 2205-based steel with improved properties.

2. Experimental Procedure

2205 stainless steels without Al and with Al (0.5, 1, 1.5, 2, and 2.5 wt.%) were used as experimental alloys. Powders of the alloying elements were weighted and dry-mixed in a ball-mixing mill with Al₂O₃ spheres at a speed of 150 rpm for 8 hours. The mixed powders were pressed and compacted in a steel mould and then melted by arc-melting in a vacuum arc-melting furnace and casted as ingots. To obtain a uniform microstructure, the ingots were melted 3-4 times. The actual chemical compositions of the alloys with different Al contents were analysed by an X-ray fluorescence spectrometer, as shown in Table 1.

The 2205 stainless steels with different Al content ingots were heated at 1150°C for 30–40 min and then pressed as plates under 20 MPa pressure with a thickness reduction of 55–58%. Then, the steels were heated to 1170–1200°C for 20–30 min and hot-rolled as plates with a thickness of 3 mm by handle-rolling equipment to obtain a thickness reduction of 30–40%. The hot-rolled 2205 stainless steels with different Al contents were homogenized at 1090°C for 30 minutes and then water-quenched to room temperature.

The hot-rolled specimens were polished with 2000-grit emery papers, mechanically polished and etched in a solution of FeCl₃ + 30HCl + 100H₂O. The phase and microstructures of the as-casted and solution-treated specimens were examined by optical microscopy, scanning electron microscopy (SEM; model JSM-6700F, JEOL, Japan) attached to energy dispersive spectroscopy (EDS) and D8, and advance X-ray diffraction using Cu Kα radiation. Some related SEM images were quantitatively examined by Ipwin 6 software, and the amount of ferrite phase relative to the whole was taken as its volume fraction.

Tensile specimens with a thickness of 1.2 mm, length of 10 mm, and width of 2.2 mm were cut from steel plates by a line-cutting machine and polished using 600-grit SiC paper. Tensile tests were carried out at room temperature using a universal material mechanical properties tester with a tension speed of 0.2 mm/min and repeated three times to ensure obtaining a reasonably representative value of each mechanical property. The elongation was measured and calculated using the Chinese GB/T 228-2002 standard method. Three specimens of each steel were tested, and average values of the yield strength, tensile strength, and elongation rate were obtained. The data deviation was less than 10%.

Specimens with dimensions of 15 mm × 10 mm × 3 mm were cut from the steel plates and polished using 1000-grit SiC paper. The specimens were exposed at 1000°C in air for 100 h in a heat-resisting furnace. The mass loss of the specimens before and after the exposure was measured by an electronic balance with a precision of 0.1 mg according to the Chinese GB/T 13303-1991 standard method. Three specimens of each type of steel were tested, and average values were obtained. The data deviation was less than 10%.

Steel specimens with dimensions of 15 mm × 10 mm × 3 mm were cut and polished using 1000-grit SiC paper. Corrosion resistance tests were carried out in a 5% H₂SO₄ solution for 8 h, and then the specimens were cleaned by an ultrasonic cleaner in distilled water. The mass loss of the specimens before and after the corrosion was measured by an electronic balance with a precision of 0.1 mg using the Chinese GB/T 4334.6-2000 standard method. Three specimens of each type of steel were tested, and average values were obtained. The data deviation was less than 10%.

3. Results

Figure 1 shows X-ray diffraction patterns of the alloys without and with 1.0, 1.5, and 2.0 wt.% Al. It can be found that the alloys are composed of ferrite and austenite phases. The peak intensity of the ferrite phase increases with the increasing Al content. Other Al-rich phases were not observed by XRD.

Figure 2 illustrates the optical microstructures of the alloys with different Al contents. It can be found that the microstructures consist of a dark ferrite phase and a bright austenite phase. The volume fraction of the ferrite of the alloy with 0.5 wt.% Al is slightly lower than that of the alloy without Al. When the Al content of the alloys is more than 0.5 wt.%, the volume fraction of the ferrite gradually increases in the alloys (Table 2). The islands of ferrite phase are uniformly distributed in the austenite matrix when the Al content of the alloys is less than 1.5 wt.% while the ferrite grain size is in the range of 10–100 μm. The shape of the austenite phase transformed from the matrix to islands with the increasing of the Al content from 1.5 to 2.5 wt.%, leading it to be uniformly distributed in the ferrite matrix. The average grain size of the austenite is in the range of 10–20 μm. The ferrite volume fractions in the alloys with different Al contents were calculated to be approximately 0.35, 0.2, 0.46, 0.71, 0.77, and 0.86, respectively.

(a)

(b)

(c)

(d)

(e)

(f)

Figure 3 shows the distributions of the alloying elements in the alloys with 0.5 and 1.5 wt.% Al, where most of Al is uniformly distributed in the ferrite and austenite phases. However, a few tiny black inclusions composed of Mn and Al exist in the alloy with 1.5 wt.% Al. Figure 4 shows tensile stress-strain curves of the alloys with different Al contents. The yield and ultimate tensile strength obtained from the curves and elongation rates of the alloys are shown in Figure 5. The ultimate tensile strength and elongation rate of the alloys increase at first and then decrease with the increasing Al content. The alloy with 0.5 wt.% Al has the highest ultimate tensile strength of 780 MPa and an elongation rate of 55%. The ultimate tensile strength and elongation rate of the alloys without Al and with 1.0 wt.% Al are almost the same, and the yield strength of the alloys with Al contents in the range of 0.5 to 2.0 wt.% also does not significantly change. The alloy with 2.5 wt.% Al has the highest yield strength (607 MPa) but the lower ultimate strength, which must be related to a low work hardening capacity of this alloy.

(a)

(b)

(a)

(b)

Figure 6 shows oxidizing kinetics curves and the oxidation rates of the alloys with different Al contents as function of exposure time. The oxidation rates of the alloys dramatically decrease with the increasing Al content, reaching a minimum value at 1.5 wt.% Al and then slowly increasing. The oxidation rate of the alloy with 0.5 wt.% Al is slightly lower than that of the alloy without Al. The oxidation rate of the alloy with 1.5 wt.% Al is 0.3401 g/m²·h, approximately 10 times lower than that of the alloy without Al.

(a)

(b)

Figure 7 shows the oxidation surfaces of the alloys. Those of the alloys with 1.0 and 1.5 wt.% Al are covered by a uniform and dense oxide scale, whereas cracks and pores appear on the surface of the alloy with 0.5 wt.% Al. This result is consistent with the change in the oxidation resistance of the alloys. Figure 8 shows that the corrosion rates of the alloys with 0.5 and 1.0 wt.% Al are slightly higher than that of the alloy without Al. On the other hand, the corrosion rates of the alloys with 1.5, 2.0, and 2.5 wt.% Al are much higher than the others.

(a)

(b)

(c)

4. Discussion

Because the solid solution limits of Al in the bcc ferrite and fcc austenite phases are higher than 10 wt.% according to Fe-Cr-Ni-Al phase diagram, the Al in the steels with different contents of Al was dissolved in the ferrite and austenite, and no Al-rich phase was observed [21]. Al is a strong ferrite stabilizer, so the volume fraction of the ferrite in the alloys could gradually increase with the increasing Al content, although that of the alloy with 0.5 wt.% Al was less than that of the alloy without Al. This can be explained by the fact that the bonding energy of Al-N is higher than that of Fe-N, which causes the diffusion coefficient of N in the Fe to decrease due to the addition of Al and the solid solubility of N in the matrix to increase because the escape of N from the matrix was hampered [22]. N is a strong austenite stabilizer. The increased solid solubility of N in the matrix contributed to the increase of the austenite volume fraction in the alloy with 0.5 wt.% Al. With the increasing of the Al content from 1 to 2.5 wt.%, the solid solubility of Al in the matrix improved, which accelerated the formation of the ferrite phase.

The yield strength of the alloys gradually increased when the Al content is more than 1.5 wt.%, which can be attributed to the solid solution strengthening effect of Al element [23]. However, there exists a clear relationship between the YS and ferrite volume fraction in the alloys with Al, with the YS increasing gradually with the Al content. The ferrite phase is regarded as stronger than the austenite phase, which causes the addition of Al to enhance the YS of the alloys [24].

The ultimate tensile strengths and elongation rates of the alloys with different Al contents increased at first and then decreased. The alloy with 0.5 wt.% Al has higher values than that without Al, which is attributed to the increasing volume fraction of the austenite phase. It was reported that strain hardening has a much greater influence on the UTS than the chemical composition [25], and strain hardening is related to the dislocation strengthening mechanism [26].

The SFE of the austenite phase is reduced due to the solid solution containing more N in the austenite, which contributes to planar slip and enhances the ultimate tensile strength [27]. When the Al content of the alloy is more than 1 wt.%, the ultimate tensile strength and elongation rate of the alloys are significantly reduced compared to those of the alloy without Al. The reason for this phenomenon is that the ultimate tensile strength of the austenite phase is higher than that of the ferrite phase, which lowers the ultimate tensile strength of the high-Al alloys.

The oxide scale on the alloy surface plays a key role in the oxidation resistance [28]. With the increasing Al content, the Cr₂O₃ scale on the alloy surface gradually decreases and the Al₂O₃ increases. It is well known that the thermodynamic stability of the Al₂O₃ scale is superior to that of the Cr₂O₃ scale [29]. Hence, the oxidation rate of the alloys gradually decreases with the increasing Al content up to 1.5%. The lowest oxidation rate of the alloy with 1.5 wt.% Al is due to its best oxidation surface morphologies, as shown in Figure 7(c). The oxidation rates of the alloys with 2 and 2.5 wt.% Al are slightly increased, which may be related to the diffusion rates of the alloying elements.

The passive film plays a significant role in the corrosion of 2205 in acid reducing media. The passive film can prevent metal ions from diffusing. However, the presence of Al can lead to metal ion dissolution and the increase of corrosion rate may be consequence of this. Thus, the steels with 0.5 or 1.0 wt.% Al exhibited higher corrosion rates than the steel without Al. In the steels with 1.5, 2.0, and 2.5 wt.% Al, the dramatic increase in the corrosion rate can be attributed to the increased ferrite to austenite phase ratio, which would lead to galvanic action in acid reducing media [30].

5. Conclusions

(1)The ferrite volume fraction in the alloy with 0.5 wt.% Al is slightly lower than that of the alloy without Al, but it gradually increases with the Al content in the range of 0.5 to 2.5 wt.%, and the morphology of the ferrite transforms from islands to a continuous matrix. Most of Al in the steels was dissolved in the ferrite and austenite phases.(2)The ultimate tensile strength and elongation of the alloy with 0.5 wt.% Al are higher than those in the alloy without Al, but they decreased as the Al increases from 0.5 to 2.5 wt.%.(3)The alloys with Al have much better oxidation resistance than those without Al owing to the formation of Al₂O₃ oxidation scale on the alloy surface. The alloy with 1.5 wt.% Al had the best oxidation resistance, approximately 10 times lower than that of the alloy without Al. The corrosion rates of the steels with 0.5 to 1.0 wt.% Al were slightly lower than that of the alloy without Al, but those of the other alloys were much higher.

Competing Interests

The authors declare that they have no competing interests.

Acknowledgments

The work is supported by the Natural Science Foundation of China (51561020), the Youth Science Foundation of Lan Zhou Jiao Tong University (2012016), and the Natural Science Foundation of Gansu (214176).

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Copyright © 2016 Qian Meng et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

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