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Investigation on Explosive Welding of Zr 53 Cu 35 Al 12 Bulk Metallic Glass with Crystalline Copper Jianrui Feng, Pengwan Chen, and Qiang Zhou (Submitted December 27, 2017; in revised form April 13, 2018; published online May 7, 2018) A Zr 53 Cu 35 Al 12 bulk metallic glass (BMG) was welded to a crystalline Cu using explosive welding tech- nique. The morphology and the composition of the composite were characterized using optical microscopy, scanning electron microscopy, energy-dispersive x-ray spectroscopy and transmission electron microscopy. The investigation indicated that the BMG and Cu were tightly joined together without visible defects, and a thin diffusion layer appeared at the interface. The captured jet at the end of the welding region mostly comes from the Cu side. Amorphous and partially crystallized structures have been observed within the diffusion layer, but the BMG in close proximity to the interface still retains its amorphous state. Nanoin- dentation tests reveal that the interface exhibits an increment in hardness compared with the matrix on both sides. Keywords bulk metallic glass, copper, explosive welding, microstructure, nanoindentation 1. Introduction Bulk metallic glasses (BMGs) are technologically one new class of solid metallic materials with many excellent properties, such as high specific strength, hardness, wear resistance and corrosion resistance as compared with crystalline materials (Ref 1). This can be attributed to their disordered atomic structure (Ref 2, 3). These excellent properties make BMGs special and potentially game-changing materials in many fields. However, the undesirable brittleness properties and the size limitation will seriously constrain their applications (Ref 4, 5). To solve the size problem and extend their applications, many research efforts have been devoted to weld amorphous materials with crystalline alloys. In addition, the composite plates between BMGs and other crystalline materials can obstruct the spread of shear bands and improve the strength–plasticity performance (Ref 6). Therefore, in the past years various welding tech- niques, including explosive welding (Ref 7-10), electron-beam welding (Ref 11-14), friction stir welding (Ref 15-18) and laser welding (Ref 19), have already been used to join BMGs with other materials. Explosive welding is well known for its capability to join a wide variety of both similar and dissimilar metals, which can hardly be joined using any other welding techniques (Ref 20, 21). The plates, tubes or bars of large dimensions can be easily fabricated using this method, which possess unique and advantageous properties, such as low weight, high corrosion resistance, high-temperature resistance, high frictional proper- ties and excellent mechanical strength. Because of the charac- teristic feature of the fast welding process, explosive welding is an effective method to reduce the formation of brittle inter- metallics (Ref 22). Until now, many material combinations, including Al-Cu (Ref 23), Ti-steel (Ref 24), Cu-steel (Ref 25), W-Cu (Ref 26) and even multilayers of metals such as Mg-Al- Ti-Cu-Mo (Ref 27), have been welded together using explosive welding technique. Therefore, explosive welding seems to be an ideal welding method for joining bulk metallic glasses. So far, some attempts have already been made to weld metallic glass with other metallic materials using explosive welding. Chiba et al. (Ref 7, 8) welded Zr 41.2 Ti 13.8 Cu 10 Ni 12.5 Be 22.5 bulk metallic glass to crystalline metallic plates using explosive welding. After welding, they found that the BMGs still retained their amorphous structure and original mechanical properties. Liu et al. (Ref 9) welded Ti 40 Zr 25 Cu 12 Ni 3 Be 20 bulk metallic glass with 1060 aluminum plate and confirmed that the plates are joined together at an atomic scale. Jiang et al. (Ref 10) achieved a strong metallurgical bonding between Zr 41.2 Ti 13.8- Cu 12.5 Ni 10.0 Be 22.5 bulk metallic glass and a commercial Cu- based crystalline alloy using thick-walled cylinder explosion technique. All of the results confirmed that explosive welding is an effective method to join BMG with crystalline materials. However, the microstructure and mechanical properties of the composite plates still need further investigation. For this purpose, in this paper, a composite plate of Zr 53 Cu 35 Al 12 bulk metallic glass and crystalline copper was obtained using the explosive welding technique. After welding, their microstructure evolution at the interface and the mechan- ical properties of the welded joint were investigated. 2. Experimental Procedures Zr 53 Cu 35 Al 12 BMG (30 mm 9 20 mm 9 2.5 mm) and pure copper (100 mm 9 50 mm 9 1 mm) plates were used for explosive welding. The ingots of Zr 53 Cu 35 Al 12 (at.%) were prepared by arc melting from the pure elements with a purity of 99.9% or better under a Ti-gettered argon atmosphere. The amorphous nature of the BMG was confirmed by x-ray diffraction (XRD) and differential scanning calorimetry (DSC) (Fig. 5). It should be mentioned that BMGs usually Jianrui Feng, Pengwan Chen, and Qiang Zhou, State Key Laboratory of Explosion Science and Technology, Beijing Institute of Technology, Beijing 100081, PeopleÕs Republic of China. Contact e-mail: [email protected]. JMEPEG (2018) 27:2932–2937 ÓASM International https://doi.org/10.1007/s11665-018-3396-5 1059-9495/$19.00 2932—Volume 27(6) June 2018 Journal of Materials Engineering and Performance

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Page 1: Investigation on Explosive Welding of Zr53Cu35Al12 Bulk Metallic …shock.bit.edu.cn/docs/20180913090736881668.pdf · 2018-09-13 · Investigation on Explosive Welding of Zr 53Cu

Investigation on Explosive Welding of Zr53Cu35Al12 BulkMetallic Glass with Crystalline Copper

Jianrui Feng, Pengwan Chen, and Qiang Zhou

(Submitted December 27, 2017; in revised form April 13, 2018; published online May 7, 2018)

A Zr53Cu35Al12 bulk metallic glass (BMG) was welded to a crystalline Cu using explosive welding tech-nique. The morphology and the composition of the composite were characterized using optical microscopy,scanning electron microscopy, energy-dispersive x-ray spectroscopy and transmission electron microscopy.The investigation indicated that the BMG and Cu were tightly joined together without visible defects, and athin diffusion layer appeared at the interface. The captured jet at the end of the welding region mostlycomes from the Cu side. Amorphous and partially crystallized structures have been observed within thediffusion layer, but the BMG in close proximity to the interface still retains its amorphous state. Nanoin-dentation tests reveal that the interface exhibits an increment in hardness compared with the matrix onboth sides.

Keywords bulk metallic glass, copper, explosive welding,microstructure, nanoindentation

1. Introduction

Bulk metallic glasses (BMGs) are technologically one newclass of solid metallic materials with many excellent properties,such as high specific strength, hardness, wear resistance andcorrosion resistance as compared with crystalline materials (Ref1). This can be attributed to their disordered atomic structure(Ref 2, 3). These excellent properties make BMGs special andpotentially game-changing materials in many fields. However,the undesirable brittleness properties and the size limitation willseriously constrain their applications (Ref 4, 5). To solve thesize problem and extend their applications, many researchefforts have been devoted to weld amorphous materials withcrystalline alloys. In addition, the composite plates betweenBMGs and other crystalline materials can obstruct the spread ofshear bands and improve the strength–plasticity performance(Ref 6). Therefore, in the past years various welding tech-niques, including explosive welding (Ref 7-10), electron-beamwelding (Ref 11-14), friction stir welding (Ref 15-18) and laserwelding (Ref 19), have already been used to join BMGs withother materials.

Explosive welding is well known for its capability to join awide variety of both similar and dissimilar metals, which canhardly be joined using any other welding techniques (Ref 20,21). The plates, tubes or bars of large dimensions can be easilyfabricated using this method, which possess unique andadvantageous properties, such as low weight, high corrosionresistance, high-temperature resistance, high frictional proper-ties and excellent mechanical strength. Because of the charac-teristic feature of the fast welding process, explosive welding is

an effective method to reduce the formation of brittle inter-metallics (Ref 22). Until now, many material combinations,including Al-Cu (Ref 23), Ti-steel (Ref 24), Cu-steel (Ref 25),W-Cu (Ref 26) and even multilayers of metals such as Mg-Al-Ti-Cu-Mo (Ref 27), have been welded together using explosivewelding technique. Therefore, explosive welding seems to bean ideal welding method for joining bulk metallic glasses. Sofar, some attempts have already been made to weld metallicglass with other metallic materials using explosive welding.Chiba et al. (Ref 7, 8) welded Zr41.2Ti13.8Cu10Ni12.5Be22.5 bulkmetallic glass to crystalline metallic plates using explosivewelding. After welding, they found that the BMGs still retainedtheir amorphous structure and original mechanical properties.Liu et al. (Ref 9) welded Ti40Zr25Cu12Ni3Be20 bulk metallicglass with 1060 aluminum plate and confirmed that the platesare joined together at an atomic scale. Jiang et al. (Ref 10)achieved a strong metallurgical bonding between Zr41.2Ti13.8-Cu12.5Ni10.0Be22.5 bulk metallic glass and a commercial Cu-based crystalline alloy using thick-walled cylinder explosiontechnique. All of the results confirmed that explosive welding isan effective method to join BMG with crystalline materials.However, the microstructure and mechanical properties of thecomposite plates still need further investigation.

For this purpose, in this paper, a composite plate ofZr53Cu35Al12 bulk metallic glass and crystalline copper wasobtained using the explosive welding technique. After welding,their microstructure evolution at the interface and the mechan-ical properties of the welded joint were investigated.

2. Experimental Procedures

Zr53Cu35Al12 BMG (30 mm 9 20 mm 9 2.5 mm) andpure copper (100 mm 9 50 mm 9 1 mm) plates were usedfor explosive welding. The ingots of Zr53Cu35Al12 (at.%) wereprepared by arc melting from the pure elements with a purity of99.9% or better under a Ti-gettered argon atmosphere. Theamorphous nature of the BMG was confirmed by x-raydiffraction (XRD) and differential scanning calorimetry(DSC) (Fig. 5). It should be mentioned that BMGs usually

Jianrui Feng, Pengwan Chen, and Qiang Zhou, State KeyLaboratory of Explosion Science and Technology, Beijing Instituteof Technology, Beijing 100081, People�s Republic of China. Contacte-mail: [email protected].

JMEPEG (2018) 27:2932–2937 �ASM Internationalhttps://doi.org/10.1007/s11665-018-3396-5 1059-9495/$19.00

2932—Volume 27(6) June 2018 Journal of Materials Engineering and Performance

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cannot bear large deformation (particularly in tension). Thus,fracture will occur because of the generated tensile waves underhigh-speed collision of BMGs with other solids (Ref 28, 29).Therefore, it is hard to directly join metallic glasses withcrystalline metals using the common explosive weldingmethod. To avoid fracture, before welding the Zr53Cu35Al12BMG was tightly embedded in a copper base block (100 mm 950 mm 9 10 mm). Figure 1 illustrates the sketch of the initialconfiguration. The upper surfaces of the BMG and the copperblock were kept on the same horizontal plane. Four supports,with 1 mm in height, were put on each corner of the copperblock to support the copper flyer plate. Rock-expandedammonium nitrate layer with a thickness of 10 mm was spreadon the flyer plate. The density of the explosive was 0.85 g/cm3,and the detonation velocity was approximately 3200 m/s. Anelectric detonator was inserted in the left part of the explosive,as shown in Fig. 1. By triggering the electric detonator, thedetonation was initiated, and the pure copper plate wasaccelerated toward the BMG.

After welding, the specimen for the microstructure obser-vation was obtained by cutting the resulted product parallel tothe explosion direction. The specimens for material character-ization were prepared using the standard metallographictechnique. The microstructure examinations of the sampleswere carried out using optical microscopy, scanning electronmicroscopy (SEM, Hitachi S4800) and high-resolution trans-mission electron microscopy (HRTEM, JEM-2010). A speci-men with a thickness of 60 lm for HRTEM characterizationwas prepared and was thinned using a cryo-focused ion beam(FIB) instrument at liquid nitrogen temperature. The elementalcomposition near the interface was investigated using SEM inconjunction with energy-dispersive x-ray spectrometry (EDS,NORAN system 7). The structure of BMG was characterizedthrough XRD patterns by using a Rigaku SmartLab x-raydiffractometer with a Cu Ka radiation source (k = 1.541 A) at aworking voltage of 40 kV and working current of 40 mA. Toexplore the thermal property of the BMG, DSC analysis wasperformed using NETZSCH DSC instruments at a heating rateof 10 �C/min. Nanoindentation was conducted across theinterface using Agilent Nano Indenter G200 with the maximumdepth of 1 lm at a loading rate of 10 nm/s. The measurementswere taken along the line perpendicular to the interface (threeseries). The elastic modulus can be calculated from thenanoindentation results, given by

dP

dh¼ 2

ffiffiffi

Apffiffiffi

pp 1� v2s

Esþ 1� v2i

Ei

� ��1

ðEq 1Þ

where P is load, h is the related displacement, A is the pro-jected contact area between the sample and the indenter, vs

and vi are Poisson�s ratios of the sample and the indenter, andEs and Ei are the elastic modulus of the sample and theindenter.

3. Results and Discussion

Using the explosive welding method, the Cu and BMG aretightly joined together, and no cracks are observed at the BMGside (Fig. 2a). An optical micrograph of the bonding interfaceis shown in Fig. 2(b), indicating that an almost flat interface hasbeen formed, and no visible defects like pores or cracks arefound. It should be mentioned that because BMGs are typicallyquite brittle in tension, they are prone to break when they aresubjected to strong tension. By embedding the BMG into thecopper block in our experiment, a part of compression wavewas transmitted into the copper block, and correspondingly aweakened tension wave was reflected from the bottom surfaceof the BMG, thus effectively avoiding the fracture.

To observe the morphology and microstructure of thebonding interface at high magnification, SEM was used tocharacterize the bonding interface as shown in Fig 3(a). Itindicates that a clear transition layer with a thickness ofapproximately 2.5–3.5 lm has been formed. The elementalcompositions of the diffusion layer and BMG were measuredusing EDS at the positions marked with A and B, respectively,in Fig. 3(a). As confirmed by EDS analysis, the region at theBMG side consists of 52% Zr, 35% Cu and 13% Al (in atomicpercent), which is almost identical to the composition of the

Fig. 1 A scheme of explosive welding experiments

Fig. 2 (a) Photograph of the BMG-Cu bimetal prepared by theexplosive welding technique. (b) Optical micrograph of the jointcross section (9 100)

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BMG sample. In contrast, the composition within the diffusionlayer contains on average 36% Zr, 55% Cu and 9% Al. Todetermine the elemental distribution across the bonding inter-face, element line scan was conducted from the BMG to thecopper. The result indicates the occurrence of atomic interdif-fusion across the bonding interface (Fig. 3b). At the bondinginterface from the copper side to the BMG, the concentration ofCu element decreases linearly, whereas the concentrationgradients of the Zr and Al elements display an opposite trend.For explosive welding, interdiffusion is a key mechanism ofwelding in forming composites made of dissimilar materials,and the joining quality depends crucially on the atomicdiffusion across the interface (Ref 6). During the drasticcollision, high temperature will be generated at the weldedinterface, which is probably higher than the melting points ofthe welding plates (Ref 31). As a result, the atomic diffusioncoefficient will increase because of the accumulated hightemperature, thus leading to the formation of diffusion layer.

It is generally accepted that jet phenomenon is an essentialcondition for explosive welding. In practice, the surfacecontaminant, oxides and impurities can be stripped away bythe high-speed jet, which contributes to a tight joining (Ref 30).However, because of the fast welding process, it is quitedifficult to directly observe the ejected jet in the experiment.Until now, the jet formation and its composition are mainlyinvestigated through numerical simulation. Based on thesimulation, one can conclude that the jet comes from both the

flyer and the base plate, but mainly from the metals with lowerdensity and hardness (Ref 31, 32). In our experiment, byinserting the BMG into the copper block, after welding a smallamount of retained jet can be observed surrounding the bondinginterface, as shown in Fig. 4. Some BMG particles of less than10 lm are observed in the accumulated jet. The elementalcomposition in the position marked with C in the jet comprises24% Zr, 70% Cu and 6% Al. Similar to the simulation results,we can conclude that for the explosive welding of Zr53Cu35Al12BMG with crystal Cu, the jet comes from both the Cu and theBMG and mainly from the Cu side. However, in view of theclose density but quite different hardness of the Cu (8.9 g/cm3

and 1.99 GPa) and the BMG (6.9 g/cm3 and 7.76 GPa), we canfind that during the drastic collision in explosive welding,probably the jet is mostly influenced by the hardness of thematerial.

Based on the results mentioned above, it is reasonable toconclude that it is the high temperature that results in atomicinterdiffusion which joins plates together. However, the hightemperature at the interface might change the atomic structureof the BMG. In a bid to check whether crystallization occurs onthe BMG side, XRD and DSC analyses were conducted.Figure 5(a) shows typical XRD patterns obtained from theBMG samples before and after welding. After welding, a broadhalo peak is still present on the XRD pattern, and no crystallinediffraction peak is detected. In the DSC curves (Fig. 5b), theexothermic peaks can be clearly observed without obvious shiftin glass transition temperature (Tg= 702 K) and crystallizationtemperature (Tx= 766 K), and no marked differences in thermalproperties have been observed. The XRD and DSC resultsindicate that no crystallization occurred after welding, and theBMG still remained its original amorphous structure. In thepresent study, the impact velocity of the copper plate was about1000 m/s. Thus, a shock wave with a particle velocity of lessthan 1000 m/s was generated and transmitted into the BMGplate. In this situation, a high temperature, which is approx-imately 600 K, was generated in the shock wave (Ref 33). Itshould be mentioned that the glass transition temperature ofZr53Cu35Al12 BMG is 702 K (Fig. 5b), which is higher than thetemperature achieved in the shock wave. This explains why theBMG, away from the diffusion layer, still keeps its amorphousstate.

To further characterize the interface regions, detailedHRTEM examination of the interface was carried out(Fig. 6). One may observe that the BMG and the diffusion

Fig. 3 (a) Microstructure of the bonding interface in the BMG-Cucomposite (9 2500). (b) Line scan analysis across the bonding inter-face from BMG to Cu plate

Fig. 4 Optical micrograph of the retained jet between the Cu andBMG (9 500)

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layer (Fig. 6a) as well as the diffusion layer and the Cu(Fig. 6c) are joined together at atomic scale without anydefects. To join the materials together, one needs to bring theatoms at the bonding surface at a certain distance apart whereattractive and repulsive forces are in equilibrium. Duringexplosive welding, this is achieved because of the drasticcollision of Cu and BMG plates. Amorphous and partiallycrystallized structures were observed within the diffusion layerin Fig. 6(b). Interestingly, the sublayers with different levels ofcrystallization were detected. Phase nature of the joint wasinvestigated in the following three positions: the diffusion layerclose to the Cu side (Fig. 7a), the diffusion layer close to BMGside (Fig. 7b) and the region of BMG near the diffusion layer(Fig. 7c). Selected area electron diffraction analysis (Fig. 7a)indicates that the nanograins are identified as Cu phase. It isassumed that it is the high temperature that results in theformation of nanograins. Because of the atomic interdiffusion,amorphous structures along with partial crystallization weredetected in the diffusion layer close to the BMG side (Fig. 7b).However, at the BMG side near the interface, the metallic glassstill retains its original amorphous state (Fig. 7c), which is inaccordance with the XRD and DSC results (Fig. 5).

Figure 8(a) shows the nanohardness and elastic modulusprofile across the bonding interface, in which the original point

of x-axis corresponds to the interface. The red curve representsthe nanohardness, and the blue one corresponds to its elasticmodulus. The original hardness of the copper and the BMGwas measured to be approximately 1.99 and 7.76 GPa,respectively. Away from the bonding interface, the hardnessof both the copper and the BMG was almost equal to theirindividual initial value. However, under the high-speed colli-sion, the hardness of both materials will increase adjacent to theinterface. Likewise, because of the hardening effect, theirindividual elastic modulus near the interface will also increase.At the interface, the hardness approaches a peak value

Fig. 5 XRD patterns (a) and DSC curves (b) of the BMG beforeand after welding

Fig. 6 High-resolution TEM images showing the microstructure atthe interface of the explosively welded BMG and Cu

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(8.81 GPa), which is higher than those of both Cu and BMG.This is possibly due to the formation of nanoparticles in thebonding interface. Because of the low modulus and highhardness characteristic of BMG, the hardness of BMG is muchhigher than the copper plate, but the modulus of the BMG islower than the copper plate. Corresponding load–depth curvesare also presented in Fig. 8(b), from which we can clearly findthe different mechanical response among the copper plate (I),the interface (II) and BMG (III).

4. Conclusion

In this paper, the Zr53Cu35Al12 BMG-Cu composite wassuccessfully obtained using the explosive welding technique.By placing the BMG into the copper block, the fracture on thebrittle BMG side can be effectively avoided. A flat and defect-free bonding interface with a thickness of 2.5–3.5 lm wasformed between the plates. Our results experimentally confirmthat the ejected jet mainly comes from the Cu side during thedrastic collision between the Cu and BMG. Vitrification andpartial crystallization were observed in the diffusion layer, butthe BMG in vicinity of the interface still retains its amorphousstate. The bonding interface exhibits an increment in hardnessin comparison with the matrix on both sides.

Acknowledgments

The authors would like to express their thanks for the financialsupport of National Natural Science Foundation of China underGrants Nos. 11521062 and 11472054.

Fig. 7 Electron diffraction patterns corresponding to the diffusionlayer near the Cu plate (a), the diffusion layer near the BMG plate(b) and the BMG plate near the interface (c)

Fig. 8 (a) Nanohardness and modulus profile across the weldedinterface. (b) Corresponding load–depth curves between copperplate, interface and BMG

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Journal of Materials Engineering and Performance Volume 27(6) June 2018—2937