Microstructural Characteristics and Mechanical Properties of 2205/AZ31B Laminates Fabricated by Explosive Welding

Abstract

A bimetal composite of 2205 duplex stainless steel and AZ31B magnesium alloy was cladded successfully through the method of explosive welding. The microstructural characteristics and mechanical properties of 2205/AZ31B bimetal composite are discussed. The interface of 2205/AZ31B bimetallic composite was a less regular wavy morphology with locally melted pockets. Adiabatic shear bands occurred only in the AZ31B side near explosive welding interface. The microstructure observed with EBSD showed a strong refinement near the interface zones. Line scan confirmed that the interface had a short element diffusion zone which would contribute to the metallurgical bonding between 2205 duplex stainless steel and AZ31B magnesium alloy. The value of micro-hardness near the bonding interface of composite plate increased because of work hardening and grain refinement. The tensile shear strength of bonding interface of 2205/AZ31B composite was 105.63 MPa. Tensile strength of 2205/AZ31B composite material was higher than the base AZ31B. There were two abrupt drops in stress in the stress–strain curves of the 2205/AZ31B composite materials.

1. Introduction

Bimetal composites can utilize the advantages of two materials, obtaining a property that a single metal cannot satisfy. Thus, bimetal composites have broad development prospects and are becoming a popular research field in material science [1]. Typical bimetal composites, such as stainless steel/carbon steel [2], titanium/steel [3], titanium/aluminum [4] and so on, have been used in a wide range of industrial fields. Magnesium alloys have wide application prospects in the automotive and transportation industries due to their low weight, high specific strength and good castability [5]. However, magnesium alloys have the intrinsic drawbacks of poor corrosion resistance and low formability [6], which limit the application of magnesium alloys. It is well known that stainless steel (STS) exhibits excellent corrosion resistance and mechanical strength, which makes it perfect for use in a wide range of industrial fields [7]. Therefore, a bimetallic macro-scale composite material comprised of magnesium alloys and stainless steels cannot only protect from the corrosion of magnesium alloys but also utilize the strength of stainless steels [8]. Besides, the characteristics of earthquake resistance and wave absorption of magnesium alloys [9,10] can make up for the deficiency of stainless steels in these areas. Stainless steels can also increase the strength, wear resistance and impact resistance of magnesium alloys [11]. We know that Fe and Mg elements are incompatible according to Mg-Fe binary alloy phase diagram [12]. Because of the difference in melting point (TM AZ31 = 630 °C and TM 2205 = 1455 °C), it is impossible to use fusion welding to melt these two kinds of metal at the same time [13]. Consequently, bonding between STS and Mg alloys is considerably restricted.

In recent years, many investigators have been involved in the study of the bonding process of magnesium alloy and steel. A variety of joining techniques have been attempted to achieve the joining of magnesium and steel. Elthalabawy and Khan [13] investigated the use of liquid phase forming interlayers to bond AZ31 to 316L. The experimental result indicated that stainless steel and magnesium alloy were successfully joined by using pure Cu interlayer at a eutectic temperature of 530 °C and pure Ni interlayer at a eutectic temperature of 510 °C. Bikulcius et al. [14] attempted to improve the corrosion resistance of magnesium alloy by sputter coating with stainless steel. Yuan et al. [15] studied diffusion-brazing technique of magnesium alloy and stainless steel. AZ31 and 304L were bonded by the diffusion-brazing process using pure copper as an intermediate layer. Miao et al. [16] investigated the mechanical properties and microstructure of AZ31 and Q235 welded joints by laser penetration brazing. They discovered that joining magnesium alloy to steel was defect-free when the laser offset was 0.6 mm and the tensile strength reached a maximum of 185 MPa. Wei et al. [17] designed a stirring pin to obtain magnesium alloy and stainless steel welding joint made using friction stir lap welding. Lee et al. [8] fabricated Mg-Al-stainless steel 3-ply clad sheet using the rolling bonding process. The above methods which require the use of high-end devices and an intermediate layer are high-cost and complex operations. In addition, these methods easily form intermetallic compounds at high temperatures [8,18].

Explosive welding (EXW) is a very useful technology to directly clad similar materials and dissimilar materials, as a large combination of metal plates is impractical to bond with conventional welding techniques [1,19]. Explosive welding can facilitate the formation of a joint at lower temperatures and restrain formation of the brittle intermetallic phases [20]. Similar and dissimilar metal and alloy combinations can be welded by using explosive welding techniques [1,2,3,4]. However, there is no report on explosive welding of magnesium alloy to stainless steel so far.

In the present investigation, 2205 stainless steel was explosive welded to AZ31B magnesium alloy. Mechanical properties such as micro-hardness, tensile shear strength and tensile strength of explosively welded composite plate were evaluated. The microstructural morphology and the elemental distribution near the weld interface were investigated by means of optical microscope (OM), scanning electron microscope (SEM) and Energy Dispersive Spectrometer (EDS). The aim of this study is to produce a composite and to examine the joining ability of 2205 stainless steel and AZ31B magnesium alloy with explosive cladding. As a result, this study is a new contribution in the field of Mg-steel laminated composite manufacturing.

2. Experimental Procedures

2.1. Materials

In this study, 2205 stainless steel sheet and AZ31B magnesium alloy sheet were used for explosive cladding. 2205 stainless steel sheet was selected as the cladding layer because of its superior corrosion resistance, AZ31B magnesium alloy sheet was chosen as parent sheet. The dimensions of 2205 and AZ31B sheets used in this study were 1000 mm × 800 mm × 2 mm and 1000 mm × 800 mm × 3 mm, respectively. The chemical compositions of 2205 and AZ31B are tabulated in

Table 1. The chemical composite (wt. %) of the 2205 stainless steel.

Element	C	Si	Cr	Mn	Ni	Mo	P	S	Fe
Wt. %	0.021	0.56	22.59	1.13	5.29	3.45	0.018	0.001	Balanced

and

Table 2. The chemical composite (wt. %) of the AZ31B magnesium alloy.

Element	Mn	Zn	Si	Fe	Al	Mg
Wt. %	0.63	1.10	0.10	0.05	3.02	Balanced

, respectively.

2.2. Explosive Cladding Process

The explosive welding process was carried out using a parallel arrangement as schematically shown in Figure 1. The surface of the flyer plate and base plate were polished with 800# SiC paper to remove the impurities. The upper surface of the flyer plate was coated with thin butter. The explosive material was flat above the butter layer and was sealed with a hard paper box whose dimensions were the same as the flyer plate. A detonator was inserted into explosive material to trigger an explosion and was placed at the edge of the flyer plate. The explosive material in this study was a mixed ammonium nitrate explosive. The detonation velocity was about 2200–2500 m/s. The explosive thickness was 25 mm. The initial gap between the flyer plate and basic plate was about 5 mm. Explosive welding parameters were chosen on the basis of empirical formulas [21].

2.3. Microstructural Work

Specimens for microstructural observations of 2205/AZ31B composite plate were prepared by standard metallographic techniques. The metallographic samples were cut parallel to the explosion direction from cross-section of the bimetallic composite plate. The AZ31B base plate was etched with an etchant consisting of 1 mL of HNO₃, 1 mL of CH₃COOH, 1 g of C₂H₂O₄ and 150 mL of deionized water. The microstructure characterization was done using an optical microscope (KEYENCE VHX-2000 (KEYENCE, Osaka, Japan). The grain sizes around the interface were analyzed using Gemini Sigma 300/VP SEM (Carl Zeiss AG, Jena, Germany) equipped with an Electron Backscattered Diffraction (EBSD) system. EDS X-ray analysis using a Gemini Sigma 300/VP SEM was used to study the chemical variations across the 2205/AZ31B composite plate interface.

2.4. Mechanical Test

To evaluate the mechanical properties of explosively welded 2205/AZ31B composite materials, a series of mechanical tests were carried out. All specimens were processed by the wire electrical discharge machining with low-speed (WEDM-LS). The microhardness values near the interface were measured on a microhardness machine (HV-1000). During the test, 100 gf load and 15 s holding time were applied. Different points were measured across the interface. Tensile tests were carried out for 2205 base metal and AZ31B base metal, and 2205/AZ31B composite material. The dimension of 2205/AZ31 composite tensile test specimen was shown in Figure 2. Tensile-shear test specimen was presented in Figure 3. The tensile shear test was carried out such that the tensile shear loading was assured along the bond interface. Fractography studies were conducted using a Gemini Sigma 300/VP SEM.

3. Results and Discussion

3.1. Macro Morphology of Composite Plate

A photograph of the explosively welded 2205/AZ31B composite plate is shown in Figure 4a. The surface of the composite plate showed no macroscopic crack except for small zones near their edges. The bad bond region was approximately 25 mm wide, which was attributed to unstable explosive energy at the beginning stages. The boundary position was not bonded as seen in Figure 4b. A similar result was reported by Mastanaiah et al. [22]. The composite plate-removing crack boundary was subjected to ultrasonic inspection according to ASTM A578M. The inspection result indicated that bonding interface was fault-free. Figure 4c presents a photograph of the cut section of the composite sheet. It was observed that the welding quality was sound, no crack and delamination were present. This demonstrated that explosive welding was an applicative technique to bond 2205 stainless steel and AZ31 magnesium alloy plates.

3.2. Morphology near the Interface

Figure 5a is a cross-section of 2205/AZ31B bimetallic composite. According to the macroscopic morphology, the 2205/AZ31B bimetallic composite had an almost-straight bonding interface. Based on the explosive weldability window theory [23], straight, wavy and melting interfaces could be formed after the explosive welding. The interface morphology is related to welding process parameters and the properties of materials. In work of Durgutlu et al. [24], the bonding interface transformed from straight to wavy with the increasing of explosive ratio and stand-off distances. No pores and cracks were observed near the interface from Figure 5a. In addition, the presented microstructure of the 2205/AZ31B interface showed that local melting zones occurred on the magnesium alloy side, resulting from the low melting point of magnesium alloy compared to stainless steel.

It can also be seen from Figure 5a that there were many adiabatic shear bands (ASBs) originating from the interface as indicated by arrows and disappearing with increasing distance from the bonding interface on the AZ31B side near the interface. Magnesium alloys are well known to easily form ASB under high strain rates such as explosive shocking, ballistic impact and high-velocity shaping [19]. It was reported that the ASB was a special case of thermoplastic instability favored by high rates of compressive strain [25]. In the explosion welding process, the strong explosion shock loading caused the high temperature, high pressure and high shear strain near the interface. The explosion time was very short, insufficient time for the heat to dissipate before thermal softening occurred, which contributed to promoting the development of ASB. No ASB was observed on the 2205 stainless steel side. Magnesium alloy (h.c.p.) had a limited slip system compared to 2205 stainless steel. Due to the crystal structure difference, stainless steel had a larger ability to accommodate the strain by dislocation movement than magnesium alloy, this was one of the reasons why ASB occurred only on the AZ31 side and not on the 2205 side. Figure 5b is a high-magnification photomicrograph of the ASB structures. It was evident that the ASB structures had fine grains. Yang et al. [26,27] reported that dynamic recrystallization was the formation mechanism of ASB after explosive welding. In high-temperature conditions, new grains nucleated and grew inside the grain. As a direct consequence, the microstructure of ASB refined.

Figure 6a presents the EBSD analysis results across the 2205/AZ31B interface, and the grain size statistics for different crystals are shown in Figure 6b–d. Finer grain is colored blue. As shown in Figure 6a, the blue grains are distributed near the interface, with the grains around the interface obviously having been refined after explosive welding. This is because the temperature and pressure at the bonding interface are fiercely raised during the explosive welding process, and remain so for a while [28,29]. Though the high temperature and pressure time are extremely short, they created an annealing effect. Thus, finer grains are formed around interface due to the rapid cooling speed.

3.3. SEM Morphology and EDS Analyses near the Interface

Figure 7 shows the SEM micrograph of the 2205/AZ31B interface. It can be observed that the bonding interface presents a less regular, wavy morphology. Mousavi and Sartangi [3] have explained the wavy forming mechanism of explosive welding interface. The less regular wavy morphology is the result of the large differences in both melting temperature and density between 2205 and AZ31B [4,30]. The wave is symmetric in the literature reported for similar materials, such as in the welding of aluminium (Al to Al) [31] and steel (stainless steel to carbon steel) [2,7]. Furthermore, as illustrated in Figure 7, irregularly distributed molten metal is observed in the vicinity of the wave-like interface, which is due to instabilities induced by the explosion. It should be noted in Figure 7 that initial oxides covering in the interface did not exist at the interface after the explosive welding. After the detonation the stainless steel flyer plate was accelerated towards the magnesium alloy plate, the jetting formed between the two plates. It removed the initial oxides or impurities from the surface of two materials, which were also described in many early reports [4,32]. The existence of such oxide film was detrimental in other connection methods such as resistance welding [33] or diffusion bonding [34], as it could decrease the bond strength of joints.

In order to discuss the distribution of elements across the bonding interface, the representative concentration profiles of Fe, Cr, Ni in the 2205 stainless steel and Mg, Al in the AZ31B are shown in Figure 8. The line scan shows that there exists a thin diffusion layer in the bonding interface. But the concentration variations of Cr, Ni and Al are difficult to reveal in the line scan because of their low concentrations. Elemental mutual diffusion indicates that metallurgical bonding of 2205 stainless steel and AZ31B magnesium alloy was achieved by explosive welding. The explosive welding process [1,2,3,4] is a “cold welding” process, and the explosion time is instantaneous (approximately 10⁻⁶ s), so there is not enough time to form a thick diffusion layer and intermetallics. This is different from liquid phase bonding in which intermetallic compounds are formed by atomic interactions as a result of a long heating time [13].

Figure 9 shows the EDS spectrum images of representative points. Quantitative analysis of the chemical compositions near the interface are listed in

Table 3. Chemical compositions (Wt. %) near interface as indicated in Figure 6.

Point	Fe	Cr	Ni	Mg	Al
1	69.80	23.80	6.40	-	-
2	70.13	23.74	5.23	0.84	0.06
3	10.72	6.61	0.61	81.54	0.52
4	0.18	0.04	0.13	98.09	1.56
5	-	-	-	97.58	2.42
6	15.68	5.00	1.06	76.94	1.32
7	12.88	4.41	1.29	80.21	1.21
8	15.05	5.29	1.16	77.30	1.20

. The chemical composition near the interface is not homogeneous as it varies depending on the EDS-analyzed zones in Figure 7. The variation trend of the chemical composition also indicates that a thin diffusion layer appears near the interface. The chemical compositions at point 1 and point 5 are in agreement with the base metals as listed in Table 2 and Table 3. Specifically, the chemical compositions at points 6 to 8 in the local melted zone largely consist of Mg, whereas relatively high Fe contents are also identified. The low melting point contributes to the preferential melting of magnesium alloy. The Fe element ejected from the 2205 sheet during the impact was captured in melting zones of magnesium alloy, resulting in a relatively high Fe content in melting zones. According to the Fe–Mg phase diagram [12], Fe and Mg elements are incompatible and cannot form any intermetallic compound. It is speculated that a non-equilibrium solid solution is formed near the interface through the Fe–Mg immiscible system [17]. The explosive welding process deviates a long way from equilibrium conditions [4]. During the explosive welding process, local high pressure and high temperature occurred near the interface, followed by grain refinement, which prompted the fast diffusion tracks (grain boundaries) for elements. Besides, the high-density dislocations near the interface were formed at the interface of metals when the explosion happened [22]. The high-density dislocations would also provide a channel for element diffusion [2,35]. Similar findings were also observed by Wei et al. [17] in the friction stir welding of stainless steel to magnesium alloy. The authors concluded that the strong plastic deformation under the action of the FSW tool promoted the mutual diffusion of magnesium and iron in the Fe–Mg immiscible system.

3.4. Microhardness Measurements

Microhardness measurements were carried out across the 2205/AZ31B bonding interface to evaluate qualitatively the microstructural changes and mechanical property variations. Figure 10 showed the results of the microhardness across the 2205/AZ31B interface after explosive welding. Obviously, the microhardness values of 2205 near the interface had the highest value. The grain refinement near the interface led to an increase in hardness near the interface. In addition, because of the difference in the thermophysical properties between stainless steel and magnesium alloy, the residual stress contributes to the hardening effect near the interface [36]. The maximum microhardness value of 2205 near the interface was approximately 380 HV, which was approximately 51% higher than the microhardness of the 2205 base material. The microhardness of 2205 over 900 μm away from the interface was 252 HV which was similar to 2205 base material. In the magnesium alloy side, the microhardness reached a maximum 136 HV near the collision surface. The microhardness of magnesium alloy over 300 μm away from the interface was 96 HV which was similar to magnesium alloy base material. It was evident that the microhardness of stainless steel near the bonding interface increased significantly, nevertheless microhardness on the side of magnesium alloy increased slightly. This was attributed to higher strain hardening of the stainless steel in comparison to the magnesium alloy. Another interesting observation in Figure 10 is that 2205 exhibited a wider hardening range than AZ31B, which was related to the higher softening temperature of stainless steel in comparison to magnesium alloy.

3.5. Tensile Strength Test Outcome

In order to evaluate the tensile strength of 2205/AZ31B bimetal macro-composite, tensile tests were carried out for the 2205 base metal, AZ31B base metal and the 2205/AZ31B composite material. Typical stress-strain curves are shown in Figure 11. The results of the tensile tests are also summarized in

Table 4. Tensile strength test outcome.

Material	Yield Strength (Mpa)	Ultimate Tensile Strength (Mpa)	Elongation (%)
2205 base metal	560.6	716.6	28.3
AZ31B base metal	160.75	237.9	11.6
2205/AZ31B composite	-	486.6	15.5

. In Figure 11, the results illustrate that the tensile strength of the 2205/AZ31B composite material is higher than the AZ31B base metal, which was the weaker material of the two dissimilar base materials. Two stress drops were seen from the stress–strain curves of the 2205/AZ31B composite material. According to the fracture macrostructure of composite materials shown in Figure 12b, a reduced stress phenomenon in the first stage of the tensile process was caused by the fracture of the AZ31 side. Soon afterwards, interface delamination occurred when stress increased, as seen in Figure 12c. In the end, the 2205 stainless steel fractured. The poor plastic deformation ability of magnesium alloy led to fracture from the AZ31 side in the first stress drop. It can clearly be seen from Figure 11 that there is a significant span in the second stage of the tensile process, which accompanied the intense necking effect in the 2205 side (Figure 12d). The good toughness of 2205 stainless steel resulted in a significant span in the second stage. The very high difference in toughness between magnesium alloy and stainless steel was the main reason for the delamination of the interface. The phenomenon of the two-stage fracture in tensile tests has been observed by other researchers who also studied the tensile properties of laminated composite materials [8]. Works carried out by Zhang et al. [28] on explosively joined Mg–Al composite materials and Kim et al. [37] on roll joined tri-layered Mg/Al/stainless steel clad plate had also shared similar results.

The fracture scanning was undertaken to clarify the rupture mechanisms of composite materials. The fractograph following the tensile test is shown in Figure 13. Clearly, the fractograph of the 2205 side exhibits a typical ductile fracture showing deep equiaxed dimples (Figure 13a), which confirm excellent plasticity of duplex stainless steel. As seen in Figure 13b, cleavage fracture can be discerned since there is a clear cleavage plane in the tensile fracture surface of the Mg layer, which is in conformity with the smaller elongation of AZ31B magnesium alloy.

3.6. Tensile Shear Test

Tensile shear tests were conducted for the 2205/AZ31B composite sheet to check the bond strength of interface. Figure 14 shows the typical load–displacement curve obtained from the tensile shear test of 2205/AZ31B composite sheet. The specimens before and after the tensile shear test are presented in Figure 15. The tensile shear test specimen was found to be fractured along the interface between 2205 and AZ31B. The average tensile shear fracture strength was 105.63 MPa.

Figure 16 displays the macroscopic morphology of fracture surfaces of tensile shear test. According to this figure, the morphology of fracture surfaces on both sides appeared periodic characteristics along the direction of detonation, which was attributed to the effect of variations in the velocity distribution at collision point and periodic disturbances of materials [38]. This is consistent with the less regular wavy interface as shown in Figure 7.

4. Conclusions

(1)

Explosive welding is a feasible technique to manufacture 2205/AZ31B composite plates.

(2)

The interface of 2205/AZ31B bimetallic composite has a less regular wavy morphology, with locally melted pockets. Adiabatic shear bands occurred only in the AZ31B side near explosive welding interface. The microstructure observed with EBSD showed a strong refinement near the interface zones.

(3)

Elemental mutual diffusion results in metallurgical bonding between 2205 duplex stainless steel and AZ31B magnesium alloy.

(4)

The microhardness value near the interface was higher than the original value, attributed to the violent plastic deformation and grain refinement at the collision interface.

(5)

The tensile shear strength of the bonding interface of 2205/AZ31B composite was 105.63MPa. Tensile strength of 2205/AZ31B composite material was higher than the base AZ31B.