Development of a New Cold Metal Transfer Arc Additive Die Manufacturing Process

Due to its high efficiency, cold metal transfer (CMT) arc additive manufacturing presents considerable potential in the aluminium alloy additive manufacturing industry. However, during CMT arc additive manufacturing, the surrounding air environment promotes the lateral flow of liquid aluminium and the instability of the molten pool, reduces the surface quality and material utilisation of deposition walls, and causes internal hydrogen pores and coarse columnar grains, which negatively affect the structure and mechanical properties of the deposition walls. .is study developed a CMTarc additive die manufacturing process to control the substrate material and deposition path to improve the physical properties of the deposition wall. .e experimental results indicated that the copper plates can affect molten pool flow and material formation in the additive process, minimise hydrogen pores, and refine columnar grains. .e porosity dropped from 2.03% to 0.93%, and the average grain size decreased from 16.2± 1.4 to 13.6± 1.3 μm, thereby enhancing the structure and mechanical properties of the deposition wall to attain standard additive manufacturing products.


Introduction
Arc additives present a wide range of applications in the engineering manufacturing. It is common to use the arc additive manufacturing technology to prepare nickel-aluminium intermetallic compounds or nickel-based alloys [1,2]. Productive additive manufacturing processes are pursued by manufacturing industries [3]. Process monitoring and inspection can improve the productivity of additive manufacturing [4]. CMTarc additive manufacturing is high-efficiency industrial technology. However, low deposition accuracy and structural properties limit the development of this technology. In general, pore defects are considered the main problem of aluminium alloy arc additive manufacturing [5]. Aluminium alloy pores mainly result from hydrogen, and the correlation between the number of pores and hydrogen-containing molecules is approximately linear [6]. Quantitative statistical analysis of the shape and number of pores in aluminium alloys can facilitate the understanding of the influence of deposition parameters on the alloys [7]. e deposition walls hammered between layers are believed to exhibit highly refined grains [8]. e middle area of the deposition wall mainly constitutes uniform equiaxed grains along the generation direction [9]. When the number of deposition layers increases, due to thermal cycling, columnar grains increase and grow along the generation direction [10].
A study found that the position of a welding wire is an important factor determining the effect of transition between a droplet and molten pool, for a rectangular deposition wall, and the zero-deflection welding wire presents high accurate feeding and withdrawal movements, which are beneficial for deposition [11]. Reciprocating deposition motion can be used to obtain relatively thicker walls [12]. e alternating deposition direction of welding wires is conducive to the construction of a regular deposition wall and substantially improves the uniformity and stability of deposition walls [13]. When a new layer of aluminium alloy is deposited, its adjacent layer is remelted and severely deformed [14]. A part of the deposition wall exhibits overlapping areas in the lateral direction and has a multilayer structure along the deposition velocity direction [15]. A correlation exists between the microstructure and geometric factors of aluminium alloys [16]. e strength is higher in the vertical direction than in the horizontal direction, and the elongation is almost the same [17].
Studies have reported that the arc energy influences the microstructure and mechanical properties [18]. With an increase in temperature, the internal porosity and grain size of the aluminium alloy increase, and its tensile and yield strengths gradually decrease [19]. e actively cooled deposition wall has lower surface roughness than the freely cooled deposition wall [20].
rough the heat treatment, materials with high hardness and ductility can be obtained [21]. In arc additive manufacturing, the Lorentz force, temperature gradient shear stress, plasma shear stress, and heat flow distribution on the molten pool surface are different from those in conventional additive manufacturing [22]. e full-time recording of the deposition current, voltage, material thermal cycle, and high speed arc images can be used to understand the mechanical behaviour of the molten pool [23]. e insertion process of particles materials affects the structure and organisation of the deposited walls [24]. Nanoparticles can control the solidification behaviour of high-strength aluminium alloys [25], and with nanomaterials, the ultimate tensile strength and elongation of the wall increase [26]. e structure optimisation and organisation homogenisation of the deposition wall of arc additive manufacturing can be achieved in the subsequent process [27]. Arc additive manufacturing must overcome the key problem of strengthening the structural organisation and mechanical properties of the deposition wall [28]. In general, the contact interface layer between the aluminium alloy and dissimilar metals includes a continuous layer and discontinuous layer [29]. No defects are present near the boundary between the two metals [30]. erefore, this study developed a CMT arc additive die-casting manufacturing process to overcome the disadvantages of traditional arc additive manufacturing in deposition accuracy and structural organisation performance and achieved an additive structure that meets industrial manufacturing standards.

Experimental Method.
CMT arc additive die manufacturing was executed on an integrated deposition platform. e 7075 aluminium alloy substrates were fixed at the top of the deposition platform by using positioning fixtures, and the T2 copper plates were fixed on both the sides of the deposition path. Manufacturing was conducted with an ER4043 aluminium-silicon welding wire, and the argon gas protection treatment was simultaneously performed. Table 1 presents the standard chemical composition of the 7075 aluminium alloy substrate, copper plate, and welding wire. Figure 1 shows the CMT arc additive die manufacturing device. e KUKA robot was used to assist CMT deposition to control the movement path and speed of the welding gun. e wire feeding system was used to adjust the wire feeding speed to control the deposition speed. e initial distance between the welding wire and aluminium alloy substrate remained constant, and the welding torch was positioned above the substrate during the movement and was used to feed the molten welding wire. Under the fixed path of the aluminium alloy substrate and copper plates, the welding torch layer-by-layer accumulated the aluminium-silicon alloy and finally formed the deposition wall. e copper plates were superimposed with an overlay fixture to keep the height of the plates consistent with the molten pool before deposition. Before each deposition, an infrared thermometer was used to measure the temperature of the copper plates to keep it at about 20°C, which can accelerate the heat dissipation of the molten pool during deposition. After each deposition, cold air was used to cool the deposition wall to minimise the heat input and thermal deformation. Deposition was conducted on a platform without path restriction and copper plates restriction path. e deposition length without path restriction was approximately 140 mm and 28 layers in the X and Z directions, respectively, and that with the copper plates restriction path was approximately 140 mm and 22 layers in the X and Z directions, respectively, as shown in Figure 2.
After the completion of deposition, the structural dimensions of the front and side of the CMT deposition wall were observed, and their geometric differences were compared. e pore size and distribution inside the deposition wall were observed using a CNC wire cutting machine, and the microstructure of the deposition wall was analysed using the Leica DM4M metallurgical microscope. Subsequently, the deposition wall samples of the transverse and longitudinal sections were selected for mechanical tensile tests. Finally, scanning electron microscopy (SEM) was used to observe the microstructure of the tensile fracture crack and analyse its fracture mechanism, as shown in Figure 3.

Layer Width and Layer ickness.
e layer width and thickness of the deposition wall served as the standards of additive manufacturing efficiency. Under the same deposition conditions, the layer width value was smaller when it was not lower than the preset width, and the layer thickness value was larger when it was not higher than the preset height. For the deposition wall without any path constraint, in the 1-6th layers of the deposition wall, the molten pool dynamically flowed to both the sides because air was in contact with both sides of the molten pool, and the flow velocity of the molten pool on the two sides is greater than that in the middle. e layer width of the deposition wall in the direction of interlayer accumulation became wider layer by layer, indicating a changing trend. Corresponding to the layer width, because the volume of each layer of the deposition wall was constant, the layer thickness of the    Advances in Materials Science and Engineering deposition wall in the direction of interlayer accumulation tended to decrease layer by layer. In the 7-28th layers of the deposition wall, because the trend of the dynamic flow of the molten pool in the middle and on both sides attained a dynamic balance, the layer width change trend of the deposition wall in the direction of the interlayer accumulation remained constant. Corresponding to the layer width, because the volume of each layer of the deposition wall remained unchanged, the trend of layer thickness change of the deposition wall in the direction of interlayer accumulation was constant, as shown in Figure 4.
In CMT arc additive die-casting manufacturing, for the deposition wall with the copper plates constrained path, in the 1-22nd layers of the deposition wall, the tendency of the molten pool to dynamically flow to both the sides was restricted and dynamic backflow occurred in the middle because of the surface constraint.
us, the molten pool concentrated in the set space area, and the trend of the layer width change of the deposition wall in the direction of interlayer accumulation was unchanged. Corresponding to the layer width, because the volume of each layer of the deposition wall was constant, the trend of layer thickness change of the deposition wall in the direction of interlayer accumulation remained unchanged, as shown in Figure 5.

Side Flatness and Top Surface Volatility.
e side surface flatness and top surface volatility of the deposited wall were the main standards for determining the surface quality and material utilisation of additive manufacturing. Under the same deposition conditions, the side surface flatness was close to the zero mark, the top surface volatility was smooth, and the surface quality and material utilisation of the deposition wall were high. According to the experiments, the calculation formulas for side flatness P and top surface volatility F are as follows: where Y is the deposition width of the deposition wall, Y 0 is the average deposition width of the deposition wall, Z is the height of the deposition wall above the substrate, and Z 0 is the penetration depth of the deposition wall below the substrate.
For the deposition wall without path constraints, the deposition wall distance in the direction of the deposition velocity was 142.5 mm. Because of the alternating contact between the solid and liquid phases of the layers, the side of the deposition wall was flat in the area away from the contact line, and protrusions and depressions occurred in the area near the contact line. e side surface flatness of the deposition wall was poor, the value of P was 11%, and the distribution law of the side flatness of the deposition wall in the interlayer accumulation direction was discrete distribution. Because the arc circulates at both ends during deposition, fluctuations at the top surface of the deposition wall were low at both ends, and the middle area fluctuated irregularly and slightly. e top surface fluctuation distribution of the deposition wall in the direction of the deposition velocity was the arc distribution, and the highest point was 54 mm, as shown in Figure 6.
In CMT arc additive die-casting manufacturing, for the deposition wall with the copper plates constrained path, the deposition wall distance in the direction of the deposition velocity was 142.5 mm. Because of the surface constraints, the protrusions of the deposition wall in the area around the contact line were suppressed, and the side surface flatness of the deposition wall was relatively better. But there are still some depressions in the area around the contact line. First, the high temperature molten pool cools and shrinks after touching the surface of the copper plate. Second, the deviation of the position of the copper plate causes uneven solidification of the molten pool. e value of F was 3%, and the distribution law of the side surface flatness of the deposition wall in the deposition velocity direction was uniform. Because of the copper plates' restriction and heat accumulation in the middle, the middle area was subjected to a high rate of thermal expansion, and a high bump was obtained. e top surface volatility was lower at both the ends and higher in the middle, and the top volatility distribution of the deposition wall in the direction of interlayer accumulation is the arc distribution. e highest point is 57 mm, as shown in Figure 7.
Under the same experimental conditions, for the deposition wall without the path constraints, the design of its size is mainly based on the adjustment of deposition parameters, and the adjustment interval of deposition parameters is narrow, which seriously affected the deposition quality and efficiency of the wall. Satisfying the requirements of industrial design is difficult, and under the general experimental conditions, the deposition wall surface must be processed from the addition to subtraction, which greatly hampers material utilisation. For the deposition wall with the copper plates constrained path, a fixed deposition path and deposition interval can be set before deposition. e deposition wall can be deposited with a specific size according to the copper plates position, which considerably improves its deposition efficiency. Moreover, it generally does not require the surface cutting or slight surface grinding treatment, which substantially improves the material utilisation degree.

Results and Discussion
3.1. Pore Defect Analysis. For the deposition wall without the path constraint, the pore size and distribution on its cross section are shown in Figures 8(a)-8(c). During deposition, the bottom of the molten pool is in contact with the upper layer of the weld, and other parts are in direct contact with the air. e average cooling rate of the molten pool is relatively low, and the air present in the molten pool cannot rapidly escape from the deposition wall before it solidifies, which leads to the formation of more pores in the deposition wall. In this state, the average porosity of the deposition wall is 2.03%, and the maximum pore diameter is 1.20 mm, which 4 Advances in Materials Science and Engineering seriously affects the mechanical properties of the deposition wall.
For the deposition wall with the copper plates constrained path, the pore size and distribution on the cross section of the wall are shown in Figures 8(d)-8(f ). During deposition, the bottom and top of the molten pool are in contact with the upper layer of the weld and air, respectively, and other parts are in direct contact with the copper plates on both the sides. e average cooling rate of the molten pool is relatively high, which promotes the air present as pores in the molten pool to rapidly escape from the deposition wall before the molten pool solidifies, leading to the reduction in the number of pores in the deposition wall. In this state, the average porosity of the deposition wall is 0.93%, and the maximum pore diameter is 0.55 mm, as the average density of the deposition wall increases, it has better compactness, which improves the mechanical properties of the deposition wall.

Heat-Transfer Model.
e heat-transfer method and heat-transfer rate of the molten pool during the additive manufacturing of the deposition wall are the main factors determining molten pool temperature [31]. Heat Advances in Materials Science and Engineering conduction, heat convection, and heat radiation are generally considered the methods of heat transfer of the molten pool during deposition, and the heat flux is the factor determining the heat-transfer rate of the molten pool [32]. For deposition wall without the path constraints, during deposition, the bottom of the molten pool is in contact with the deposition weld of the upper layer; the front, back, and top of the molten pool are in contact with the air; and the two sides of the molten pool and air form an air-interface heattransfer system. During deposition, the heat-transfer methods of the molten pool mainly are heat convection and radiation; heat conduction can be ignored, and the heat flux density of the molten pool can be expressed as follows: where λ is the thermal conductivity of the air, T 1 is the side temperature of the molten pool, T 2 is the air temperature, ΔL is the characteristic scale of the air, f is the convective heattransfer index, β is the coefficient of air expansion, g is the acceleration of gravity, ] is the air movement viscosity, k is the radiation heat-transfer index, σ is the Stephen-Boltzmann constant, and ε 1 is the emissivity of the deposition wall surface.
For the deposition wall with the copper plates constrained path, during deposition, the bottom of the molten pool is in contact with the deposition weld of the upper layer; the front, back, and top of the molten pool are in contact with the air; and the two sides of the molten pool and copper plates form an air-gap-interface heat-transfer system.
During deposition, the heat-transfer methods of the molten pool mainly are heat conduction and radiation; heat convection can be ignored, and the heat flux density of the molten pool can be expressed as follows: where λ is the thermal conductivity of the air, T 1 is the temperature of the side of the molten pool, T 2 is the temperature of the copper plates, α is the linear expansion coefficient of the deposition wall, L is the width of the copper plates, T is the initial temperature of the deposition wall, T 0 is the cooled temperature of the deposition wall, f is the convective heat-transfer index, β is the expansion coefficient of air, g is the acceleration of gravity, ] is the air kinematic viscosity, k is the radiation heat-transfer index, σ is the Stephen-Boltzmann constant, ε 1 is the emissivity of the deposition wall surface, and ε 2 is the emissivity of the copper plates surface. For the deposition wall without path restriction, during deposition, the heat-transfer modes of the molten pool mainly are convection and radiation; the heat-transfer density of the molten pool is small, and the cooling rate is slow. When the deviation between the transient thermal result and actual measured temperature is within 10%, then according to the transient thermal analysis, the temperature field gradient distribution of the deposition wall in the first layer is shown in Figure 9(a). At the end of the wall when the   Advances in Materials Science and Engineering single-layer deposition time is 17.5 s, the maximum temperature is 907.9°C. e temperature field gradient distribution in the 11th layer is shown in Figure 9(b). At the end of the wall when the single-layer deposition time is 17.5 s, the maximum temperature is 1056.7°C. Because of heat accumulation and the slow heat-transfer rate of the deposition wall, the temperature of the tenth layer is significantly higher than that of the first layer.
For the deposition wall with the copper plates constrained path, during deposition, the heat-transfer modes of the molten pool mainly are conduction and radiation; the heat-transfer density of the molten pool is large, and the cooling rate is fast. When the deviation between the transient thermal result and actual measured temperature is within 10%, then according to the transient thermal analysis, the temperature field gradient distribution of the deposition wall in the first layer is shown in Figure 9(c). At the end of the wall when the single-layer deposition time is 17.5 s, the maximum temperature is 715.01°C. Compared with the deposition wall without path restriction, for the deposition wall with path restriction, the maximum temperature considerably decreases, and the temperature gradient increases. e temperature field gradient distribution in the 11th layer is shown in Figure 9(d). At the end of the wall when the single-layer deposition time is 17.5 s, the maximum temperature is 727.97°C. Because of heat accumulation and the fast heat-transfer rate of the deposition wall, the temperature of the tenth layer is slightly higher than that of the first layer.

Pore Nucleation and Growth.
e molten pool of the deposition wall dissolves a large amount of hydrogen during additive manufacturing. During molten pool cooling, hydrogen precipitation is the essential factor for the formation of pores. e cooling rate of the molten pool is the main factor determining the number of pore nucleation per unit time [33]. During nucleation, the pores are subjected to air pressure, molten pool liquid pressure, additional pressure caused by the surface tension of the pore liquid, and electromagnetic pressure, and the internal pressure changes dynamically and is balanced with the external pressure [34]. When the nucleation radius of the pore is smaller than the critical radius, it is difficult for the pores to remain stable, and they disappear because the free energy of the gas liquid system is positively correlated with the pore radius. When the nucleation radius of the pore is smaller than the critical radius, the pores can exist stably and grow because the free energy of the gas liquid system is negatively correlated with the pore radius. e internal pressure of pore nucleation can be expressed as follows: where p a is the air pressure, ρ L is the density of the molten pool, g is the gravitational acceleration, h is the pore depth, μ 0 is the vacuum permeability, I is the current, R a is the upper radius of the arc, and R b is the lower radius of the arc. e radius of the pore nucleation can be expressed as follows: where σ 1 is the maximum surface tension, σ 2 is the minimum surface tension, p a is the air pressure, ρ L is the density of the molten pool, g is the acceleration of gravity, h is the depth of the pore, μ 0 is the vacuum permeability, I is the current, R a is the upper radius of the arc, and R b is the lower radius of the arc.  For the deposition wall without the path restriction, during deposition, the molten pool exhibits small heat exchange and a low cooling rate and forms pores at a slower nucleation rate in a longer cooling time.
For the deposition wall with the copper plates constrained path, during deposition, the molten pool exhibits large heat exchange and a high cooling rate and forms pores at a faster nucleation rate in a shorter cooling time.

Pore Movement Fusion.
During additive manufacturing, the pore movement of the molten pool of the deposition wall is mainly affected by the combined action of buoyancy and additional pressure resulting from the surface tension of the pore liquid, which is used to overcome the resistance of the molten pool liquid [35]. e movement of pores can be divided into two processes; in the initial short period of time, the pores move fast because the power is greater than the resistance, and in the subsequent long period of time, the pores move at a uniform velocity because the power of the stomata is equal to the resistance [36]. e pore velocity in the Y direction mainly results from the Y component of the additional pressure, and that in the Z direction is mainly caused by the buoyancy and Z component of the additional pressure.
e Y direction pore velocity can be expressed as follows: where σ 1 is the maximum surface tension, σ 2 is the minimum surface tension, θ is the angle between the temperature gradient direction and horizontal direction, and η is the dynamic viscosity of the molten pool. e Z direction pore velocity can be expressed as follows: where ρ L is the density of the molten pool, ρ G is the density of the gas, σ 1 is the maximum surface tension, σ 2 is the minimum surface tension, θ is the angle between the temperature gradient direction and horizontal direction, and η is the dynamic viscosity of the molten pool. For the deposition wall without the path constraint, during deposition, the heat-transfer density of the molten pool is small, and the cooling rate is slow. e molten pool exhibits a small temperature difference in the temperature gradient direction, and the additional pressure caused by the gas liquid surface tension is small. When the pore movement reaches the equilibrium state, the liquid resistance of the molten pool is small. erefore, the pore velocity in the Y direction is small, and the velocity in the Z direction is small, as shown in Figures 10(a)-10(d).
For the deposition wall with the copper plates constrained path, during deposition, the heat-transfer density of the molten pool is large, and the cooling rate is fast. e molten pool exhibits a large temperature difference in the temperature gradient direction, and the additional pressure resulting from the gas liquid surface tension is large. When the pore movement reaches the equilibrium state, the liquid resistance of the molten pool is large. erefore, the pore velocity in the Y direction is large, and the velocity in the Z direction is large, as shown in Figures 10(e)-10(h).
For the deposition wall without the path constraint, during deposition, the molten pool flows downward under the action of its gravity and flows to both the sides under the action of the arc force, thus flowing downward on both the sides. Because the molten pool flows slowly in this state and the cooling rate is slower, the molten pool forms pores at a slower nucleation rate in a longer cooling time, and the pore floating rate is small. Consequently, the internal pores escape slowly during the flow of the molten pool, which accelerates the formation of hydrogen pores in the molten pool, as shown in Figures 11(a) and 11(b).
For the deposition wall with the copper plates constrained path, during deposition, the molten pool flows downward on both the sides under the action of its gravity and arc force and flows back after coming in contact with the copper plates, causing the molten pool to flow naturally to both the sides, and then, in the opposite direction. Because the molten pool flows faster in this state and the cooling rate is faster, the molten pool forms pores at a faster nucleation rate in a shorter cooling time, and the pore floating rate is high. Consequently, the internal pores escape faster during the molten pool flow, which slows down the formation of hydrogen pores inside the molten pool, as shown in Figures 11(c) and 11(d).

Microstructure Analysis.
For the deposition wall without the path constraint, the metallographic structure of the cross section of the deposition wall is shown in Figures 12(a) and 12(b). During deposition, the bottom of the molten pool is in contact with the upper layer of weld, and other parts are in direct contact with the air. e molten pool naturally flows to both the sides under the action of arc pressure and gravity, and the surrounding pressure of the molten pool is the same as the atmospheric pressure. e high energy density of the molten pool and low undercooling lead to the presence of coarse columnar grains inside the deposition wall, with an average grain size of 16.2 ± 1.4 μm in the middle area of the height direction of the deposition wall, which attenuates the mechanical properties of the deposition wall.
For the deposition wall with the copper plates constrained path, the metallographic structure of the cross section of the deposition wall is shown in Figures 12 and  12(d). During deposition, the bottom and top of the molten pool are in contact with the upper layer of the weld and with the air, respectively, and other parts are in direct contact with the copper plates on both the sides. e molten pool flows naturally to both the sides and, then, flows in the opposite direction under the action of arc pressure and gravity. e surrounding pressure of the molten pool increases. Due to the lower energy density of the molten pool and higher undercooling, the refinement of coarse columnar grains occurs inside the deposition wall, with an average grain size of 13.6 ± 1.3 μm in the middle area of the height Advances in Materials Science and Engineering direction of the deposition wall, which improves the mechanical properties of the deposition wall.

Mechanical Behaviour.
For the deposition wall without the path constraint, the mechanical tensile strength in the deposition velocity direction and interlayer accumulation direction of the deposition wall is shown in Figure 13. e average ultimate tensile and yield strengths in the transverse section of the deposition wall are 169 and 133 MPa, respectively, and those in the longitudinal section of the deposition wall are 153 and 118 MPa, respectively. erefore, the tensile strength of the deposition wall without the path constraint is slightly higher in the horizontal direction than in the vertical direction.
For the deposition wall with the copper plates constrained path, the mechanical tensile strength in the deposition velocity direction and interlayer accumulation direction of the deposition wall is shown in Figure 14. e average ultimate tensile and yield strengths in the transverse section of the deposition wall are 203 and 162 MPa, respectively, and those in the longitudinal section of the deposition wall are 179 and 138 MPa, respectively. erefore, the tensile strength of the deposition wall with the copper plates constrained path improves in the horizontal and vertical directions.

Fracture Crack Analysis.
e area of the interlayer transition zone in the deposition velocity direction of the deposition wall is small, and that of the fracture cross section crack propagation zone in the deposition velocity direction is small, which confirms that the deposition wall strength is relatively higher in this direction. Additionally, because the area of the interlayer transition zone in the interlayer accumulation direction of the deposition wall is large, and that of the fracture section crack propagation zone in the interlayer accumulation direction is relatively larger, the deposition wall strength is lower in this direction. For the deposition wall without the path constraint, the tensile fracture surface and SEM image in the deposition velocity direction of the deposition wall is shown in Figures 15(a) and 15(b). Because the tensile fracture of the deposition wall is broken along the section with the smallest effective area in the tensile direction, the deposition wall fracture is distributed with large-scale pores, and the tensile strength of the deposition wall in this direction is low. Because smaller dimples are present on the fracture, the toughness of the deposition wall in this direction is poor. e area of the interlayer transition zone in the deposition velocity direction of the deposition wall decreases, and that of the fracture cross section crack propagation zone in the deposition velocity direction decreases, which confirms that the deposition wall strength increases in this direction. Additionally, because the area of the interlayer transition zone in the interlayer accumulation direction of the deposition wall decreases, and that of the fracture section crack propagation zone in the interlayer accumulation direction decreases, the deposition wall strength decreases in this direction. For the deposition wall with the copper plates constrained path, the tensile fracture surface and SEM image in the deposition velocity direction of the deposition wall is shown in Figures 15(c) and 15(d). Compared with the deposition wall without the constraint path, the fracture of the deposition wall with the constraint path is distributed with small-scale pores, and the tensile strength of the deposition wall in this direction is high. Because larger dimples exist on the fracture, deposition wall toughness is better in this direction.

Conclusions
is study developed a CMT arc additive die manufacturing process. Compared with wrought process, the mechanical properties of the arc additive die manufacturing parts are lower, but with the advantage of additive manufacturing. Compared with the common arc additive manufacturing process, the arc additive die manufacturing parts have been greatly improved in deposition accuracy and structural properties, and the following conclusions can be drawn from this study.
(1) e CMT arc additive die manufacturing process is developed. rough this manufacturing of the copper plates constrained path, the aluminium-silicon alloy achieves high-quality rapid prototyping and provides standard additive manufacturing products. (2) e copper plates constraint path can be used to design the layer width and thickness of the deposition wall and to control reasonable side flatness and top surface fluctuations. Side flatness decreases from 11% at the highest point to 3%, and top surface volatility increases from 54 mm at the highest point to 57 mm.
(3) e copper plates constraint path can affect molten pool flow and material formation in the additive process, lower hydrogen pores in the deposition wall, and refine columnar grains. e porosity decreases from 2.03% to 0.93%, and the average grain size decreases from 16.2 ± 1.4 to 13.6 ± 1.3 μm.

Data Availability
e data used to support the findings of this study are available from the corresponding author upon request.

Conflicts of Interest
e authors declare that they have no conflicts of interest.