Influence of Hydrogen Content on the Microstructure and Mechanical Properties of ER 5183 Wires

,is work focused on the influence of hydrogen content on the microstructure and mechanical properties of ER5183 Al-Mg-Mn alloy wires for aluminum alloy welding. ,e hydrogen content of the ER5183 wires was measured, the macroscopic and microscopic morphologies of fractures were observed as well as the microstructure of the wires, and the tensile strength of the wires was also tested and investigated. ,e experimental results demonstrated three typical irregular macroscopic fractures of the wires appeared during the drawing process when the hydrogen content exceeded 0.23 μg/g. In the meantime, the aggregated pores were observed in the microstructure of the φ5.2mmwire with the hydrogen content of 0.38 μg/g. Such defects may become the origin of cracks in subsequent processing and tensile tests. Moreover, higher hydrogen content in the φ5.2mm welding wire will bring obvious changes in the fracture surface, which are internal cracks and micropores replacing the original uniform and compact dimples. With the higher hydrogen content, the tensile strength and plastic strain rate of φ1.2mm wires would decrease. At the same time, unstable crack propagation would occur during the process of plastic deformation, leading to fracture. Considering the mechanical properties and microstructure, the hydrogen content of the ER5183 wires should be controlled below 0.23 μg/g.


Introduction
Aluminum alloys have a wide application prospect in the field of automobile manufacturing and high-speed railway due to the advantages of light density, excellent corrosion resistance, easy processing, etc. [1][2][3].Aluminum alloys have attracted widespread attention and became a new generation of structural materials in place of ferrous metal [4].In recent years, as a widely used high-strength welding material as well as the better performance in mechanical properties than ER5356, ER5183 wires play a crucial part in the reliability of aluminum alloys structural materials and are frequently used in automatic and semiautomatic GMAW (gas metal arc welding) which requires good property of wire-feeding and appearance of welding [5].Compared with other gas elements like O, N exists in the welding atmosphere and H has the highest dissolvability in aluminum alloys, which makes it the major gas element that dissolves in ER5183 wires during the solidification process [6].As a result, the microporosities and cracks are detected in the matrix of aluminum alloys semimanufactured rods [7].
erefore, the investigation on the formation mechanism of hydrogeninduced porosities and cracks in the microstructure is important to the production of qualified ER5183 wires.It is well known that a stable process is the key factor of homogeneous microstructure which is the quality guarantee of the wirefeeding property.But the porosities and cracks may cause the stress concentration under the external load and affect the homogeneity of the wires.Finally, in the situation of finished products, the combined effect of stress concentration, microcracks, and porosities worsen the mechanical properties of finished products [8].erefore, research on the influence of the hydrogen content of ER5183 wires is urgent and necessary.
Hydrogen is a common impurity that affects the microstructure as well as mechanical properties of aluminum alloys and other metals, and there were some issues about the influence of hydrogen.Lu et al. studied the properties of dislocation core with and without H impurity using the Peierls-Nabarro model.
e results showed that H has the ability of facilitating the emission of dislocation from the tip of cracks; in the meantime, they enhance the mobility of the dislocation dramatically.As a result, the macroscopically softening as well as the thinning ahead of the crack tip appeared.Besides, strong binding was observed between dislocation cores and H which inhibits dislocation cross-slip and develops slip planarity to affect the mechanical property of aluminum [9].e hydrogen content of aluminum alloys can be largely affected by the environmental humidity.Gou et al. analyzed the welded joints obtained under various humidity conditions using A7N01S-T5 aluminum alloy and found the similarity of the microstructures in both the HAZ (heat-affected zone) and the weld zone.Furthermore, the distribution of porosity was significantly affected, and the quantity of porosity increased cooperating with the humidity.Besides, the joint showed brittle fracture made under the 70% humidity while others showed ductile fracture.e result demonstrated that 70% humidity has a great possibility to be the limit humidity level for welding [10].Lu et al. found that hydrogen could cause the embrittlement in bulk aluminum under the specified condition.Vacancies could compensate the energy cost by combining with hydrogen impurities to form the defect.ree nearest single vacancies would aggregate and repel to form a trivacancy on the slip plane of aluminum with the presence of trapped H atoms.
ese vacancies could act as a birthplace for cracks and microvoids which result in the ductile fracture along the planes [11].e porosity of narrow-gap GMAW was analyzed by Zhu et al. using the 5083 aluminum alloy thick plate.
e hydrogen was found to be the major cause of the porosity.
ey adjusted heat input using the optimized parameters to avoid pores and reduce the influence of hydrogen [12].In consideration of hydrogen is the major active gas element leading to porosity in aluminum alloys, Obaldia et al. calculated the volume fraction of hydrogeninduced microporosity in castings of A356 aluminum alloy by extending a model of dendritic solidification.e simulation results are consistent with the experimental data.An online approach was also used by Yu et al. to analyze the hydrogen porosity in pulsed gas tungsten arc welding of the Al-Mg alloy.Spectral lines of H and Ar components among the arc atmosphere were analyzed, and they successfully identified the position with most probable of the native porosity and the exact position of the artificial porosity [13].
e grain size was chosen as a factor by Chou et al. to study the resistance of duplex stainless steel to hydrogen-assisted crack.e results indicated that finer grain size can decrease the susceptibility to hydrogen embrittlement and increase the tensile strength and uniform elongation of duplex stainless steels [14].
A lot of work researched the influence of hydrogen on aluminum alloys.However, very few studies focused on the microstructure and mechanical properties of aluminum alloys welding wires which are the crucial factors for the performance of aluminum welding consumable and reliability of aluminum alloy structure.erefore, the ER5183 aluminum alloy wires were chosen in this work, and the influence of the hydrogen content was discussed.e hydrogen content was measured for quantitative analysis.e macroscopic morphologies of the drawing fracture were observed to identify the mode of fracture and analyze the influence of the hydrogen content on mechanical properties.
e microscopic morphologies of the fracture and wire matrix were chosen to further research on the fracture mechanism and the role that hydrogen played.e tensile strength of both the semifinished products and the finished products was measured to study the influence of the hydrogen content on mechanical performance.
e results demonstrated the influence of hydrogen on the microstructure and mechanical properties of ER5183 wires, and the recommended content was proposed.

Production and Hydrogen Test of ER5183 Wires.
Firstly, metal ingots and additives were used for the smelting of ER5183 wires.Subsequently, in order to remove hydrogen which is abundant in raw materials, the melt was refined with hexachloroethane (C 2 Cl 6 ) and pure argon (99.99%).To determine the residual hydrogen content, the hydrogen test specimens were obtained from ϕ5.2 mm semifinished wires and measured by the hydrogen analyzer LECO RHEN602.
e schematic diagram of the hydrogen testing sample is shown in Figure 1. e finishing machining was drawingshaving to prepare the ϕ1.2 mm wires.e chemical compositions of wires which measured by the SPECTRO MAXx04D spectrometer are listed in Table 1.
e wires accord with the European standard EN 14532-3: 2004.

Tensile Test of ER5183 Wires.
After the hydrogen test, the tensile test of ER5183 ϕ5.2 mm semifinished wires was performed on a WDW-20E electronic universal testing machine (Zhejiang Jingyuan Mechanical Equipment Co., Ltd.) which operated at room temperature.After that, the samples were made into ϕ1.2mm products, and the tensile strength was tested again.e test data were obtained from three specimens and averaged.

Observation of Fracture Morphologies and Microstructure.
e stereoscopic microscope was used to observe the macromorphologies of the ϕ5.2 mm semifinished product samples after tensile tests.
e fracture morphologies and the microstructure were observed and analyzed by OM (Zeiss Axio Vert A1) and SEM (ZEISS SIGMA field-emission scanning electron microscope).

Hydrogen Content of ϕ5.2 mm Wires and the Fracture during Processing.
e hydrogen content of ϕ5.2 mm wires is shown in Table 1.
e hydrogen content ranges from 2 Advances in Materials Science and Engineering 0.18 to 0.38 μg/g which were obtained from 5 samples correspondingly.Figure 2(a) shows the process that the wire passes through the drawing die.When the wire reaches the contact position with the drawing die, the influence of the triaxial stress brings a great test of the mechanical property of the wires.e wire with the low hydrogen content (lower than 0.23 μg/g) occasionally breaks due to the issue of the production equipment and shows a ductile fracture surface in Figure 2(b) with a neck.Besides, the microstructure of the wire is homogeneous which maintains the stability during the drawing process.In the meantime, the homogeneous structure of the wires can effectively reduce the resistance of the drawing die to the wires and improve the quality of the wire surface.In contrast, three typical modes are observed in the irregular fracture surface of the wires with the high hydrogen content (higher than 0.23 μg/g): Mode I (Figure 3(a)): due to the continuous applied load during drawing processing, a stripped layer forms outside the core of the wire.As a consequence, this kind of weak structure results in the stripped skin (Figure 3(b)) under the extrusion and drawing force of the die at the contact position.Mode II (Figure 3(c)): some internal cracks (Figure 3(d)) were formed inside the wire under the applied load.Moreover, with the further deformation, those cracks decrease the continuity of the wire which reduces the effective loading area and finally cause the fracture.Mode III (Figure 3(e)): hydrogen concentrates in a certain part of the wire; as a result, defects were found both on the surface and the internal structure.Subsequently, cracks are formed at the defect, and the cracks propagate along the damaged structure, penetrating both the surface and the interior (Figure 3(f )). e fracture is dim and irregular.In addition, scratches were observed on the surface, which were caused by the resistance between the damaged tissue and the drawing die.
e molten aluminum alloy is easy to absorb gas especially vapor which contains plenty of hydrogen during the smelting process.Some H atoms are dissolved into interstitial positions in the Al matrix and trapped at vacancies.As a consequence of H trapping, the formation energy of the vacancy defect is lowered significantly, which can result in increasing in vacancy concentrations.In turn, the superabundant vacancy formation provides more trapping sites for H impurities, which effectively increases the tendency of H aggregating in bulk Al [11].

Aggregated Pores on the Microstructure of ϕ5.2 mm Wire.
EDX element mappings of the microstructure of the ϕ5.2 mm wire with the hydrogen content of 0.38 μg/g are shown in Figure 4. e aggregated pores and the white Al-Mg-Mn-Fe phase were observed.Formation of the pores is caused by the difference of the solubility of hydrogen between the solid and liquid aluminum.During the solidification of the processing, the solubility of atomic H decreases greatly.As a result, the dissolved atomic H aggregates to the H 2 molecule to escape but blocked by a rapid cooling process.e H 2 molecule unable to escape may cause the porosity.Moreover, some pores will aggregate to each other as a consequence of plastic deformation, which is shown in Figure 4(g).In the subsequent process, under the action of axial tension, the radial compression deformation occurs, and the adjacent pore gradually approaches each other, eventually joining each other to form the "aggregated pores" defect.Simultaneously, microcracks are formed around the defects.Such defects may be the origin of cracks in subsequent processing and tensile tests.

Influence of Hydrogen Content on the Tensile Strength and
the Fracture of ϕ5.2 mm Wires.Figure 5 reveals that there has been a gradual decline in the tensile strength of the ϕ5.2 mm wires with the increase of the hydrogen content.In the samples with 0.18 and 0.23 μg/g hydrogen content, the latter exhibits less than 3 MPa drop in tensile strength, which means the hydrogen has not yet given an obvious impact on the mechanical performance of the wires.However, as the     e microscopic fracture surface of the ϕ5.2 mm wires after the tensile test was chosen for further observation.In the sample with the low hydrogen content, fractures with necking and less defects are found in Figure 6(a).In the high magni cation (Figure 6(b)), the morphology mainly consists of dimples with second-phase particles.Figure 6(c) shows the case of low hydrogen content.Under the action of external loading, the necking phenomenon begins to occur in the tensile specimens, which results in the triaxial stress in the necking region.e crack nucleation and propagation will not be disturbed by hydrogen, but present a smooth process.
With the increase of the hydrogen content, the fracture surface presents an irregular and coarse appearance shown in Figure 7(a).In the high magni cation image (Figures 7(b) and 7(c)), cracks with di erent orientation were observed, respectively.Figure 7(d) reveals the details of the fracture process.Some internal cracks are thought to originate in H-rich zones.ese H-rich zones are generated by a critical local concentration of H. Excess hydrogen can promote  erefore, under the external load in the processing, the cracks can easily propagate along the newly generated slip plane.Subsequently, some internal defects begin to emerge, forming fragile areas.e fragile areas with more defects will break directly in the processing.At the same time, some defects will be retained, which will a ect the mechanical properties of the wire in the tensile test.
Secondary cracks accompanied by some black spots appeared at the fracture and in the sample with hydrogen content of 0.38 μg/g, is shown in Figure 8  6 Advances in Materials Science and Engineering the multivacancies [11].During the plastic deformation, vacancies could a ect the slip of crystal and dislocation and then generate new glide planes to avoid the obstruction.e more hydrogen the wire had, the more irregular morphology the fracture had.

In uence of Hydrogen Content on the Tensile Properties of ϕ1.2 mm
Wires. e stress-strain curves of ϕ1.2 mm wires are shown in Figure 9.It is apparent from this gure that, with the increase of the hydrogen content, tensile strength and plastic strain of the wire decrease.e ϕ1.2 mm wires had large deformation through the whole process.e relatively higher hydrogen content (0.26-0.38 μg/g) could generate more microdefects in the wires.When microdefects present in a tensile sample, they will concentrate the stress and become the origin crack source to reduce the loadbearing area.Re ected in macroperformance, the tensile strength decreases.Moreover, the e ect of Portevin-Le Chatelier (PLC) which shows as sawtooth stress yielding phenomenon is observed in those tensile specimens.
e PLC e ect is considered to be caused by the dynamic interaction between the micromovable dislocation and the solute atoms [15].When the lattice motion cannot continue in the one slip system, another slip system will start, which results in the sawtooth stress yielding.In the samples with low hydrogen content, this kind of yielding phenomenon can proceed smoothly.In contrast, due to the promotion of hydrogen on the dislocation movement, the fracture process will not absorb much energy, thus reducing the ultimate strength of the fracture.As a result, dislocations aggregate into microcracks to propagate continuously and became unstable, then caused the fracture.So, in terms of plastic strain, the specimen will not undergo much deformation before fracture.
e weak spots and the lower tensile strength would certainly cause the blocking and the instability while welding.Furthermore, the hydrogen could also enter the weld and a ects the mechanical performance.As a consequence,

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considering the microstructure and mechanical properties as well as the weldability of ER5183 wires, the hydrogen content should be controlled below 0.23 μg/g.

Conclusions
e influence of the hydrogen content on the microstructure and mechanical properties of ER5183 wires was investigated.
e conclusions are as follows: (1) e hydrogen content of the ER5183 wires ranged from 0.18 to 0.38 μg/g.e wire with low hydrogen (0.18 μg/g and 0.23 μg/g) occasionally breaks due to the issue of the production equipment and shows a ductile fracture surface.Higher content of hydrogen (0.26 μg/g, 0.32 μg/g, and 0.38 μg/g) could result in frequent fracture as well as three typical modes of irregular macroscopic fracture which might reduce production efficiency and wire quality.
(2) e aggregated pores were observed in the microstructure of the ϕ5.2 mm wire with the hydrogen content of 0.38 μg/g.Such defects may become the origin of cracks in subsequent processing and tensile tests.(3) ere has been a gradual decline in the tensile strength of the ϕ5.2 mm wires with the increase of the hydrogen content.In the sample with the low hydrogen content, fractures with necking and less defects are found.In contrast, internal cracks and micropores appeared with the hydrogen content exceeded 0.23 μg/g.(4) With the increase of the hydrogen content, the tensile strength and plastic strain rate of the ϕ1.2 mm wire decrease.Unstable crack propagation occurs in the welding wire with the high hydrogen content (higher than 0.23 μg/g) during deformation, which leads to the fracture.(5) To improve the microstructure and mechanical properties, the hydrogen content of ER5183 wires should be controlled below 0.23 μg/g.

Figure 1 :
Figure 1: Schematic diagram and macroscopic view of the hydrogen testing sample.

Figure 3 :
Figure 3: Schematic diagram and macroscopic morphology of three fracture modes: (a) Model I: stripped layer; (b) macroscopic fracture corresponding to (a); (c) Model II: internal cracks; (d) macroscopic fracture corresponding to (c); (e) Model III: crack penetrating the surface and the interior; (f ) macroscopic fracture corresponding to (e).

Figure 2 :
Figure 2: e ϕ5.2 mm wire in drawing processing and the macroscopic fracture of wires with low hydrogen content: (a) contact between drawing die and ϕ5.2 mm wire; (b) necking phenomenon of the ϕ5.2 mm with hydrogen content of 0.18 μg/g.

Figure 4 :Figure 5 :
Figure 4: e aggregated pores in the matrix of ϕ5.2 mm wire: (a) SEM micrograph of the aggregated pores; (b) EDX element mappings; (c)-(f ) the distribution of Al, Mg, Mn, and Fe, respectively; (g) schematic diagram of the aggregated pores.

Figure 6 :
Figure 6: e fracture morphology of the ϕ5.2 mm wire with hydrogen content of 0.23 μg/g: (a) macroscopic morphology of the fracture; (b) microscopic view of the dimples; (c) schematic diagram of the regular fracture.

Figure 7 :
Figure 7: e fracture morphology of the ϕ5.2 mm wire with hydrogen content of 0.26 μg/g.(a) Macroscopic morphology of the fracture; (b) and (c) microscopic view of the internal cracks; (d) schematic diagram of the H-rich zone and internal cracks.

Figure 8 :Figure 9 :
Figure 8: e fracture morphology of the ϕ5.2 mm wire with hydrogen content of 0.38 μg/g.(a) Macroscopic morphology of the fracture; (b) and (c) microscopic view of the fracture surface; (d) schematic diagram of pores leading to the formation of cracks.
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