Abstract
The twin-wire directed energy deposition-arc (TW-DED-arc) method is a low-cost and efficient in situ alloying process for producing γ-TiAl alloy, a new generation material for aero-engine blades. Its characteristic of “twin-wire-one-drop” can successfully avoid the phenomenon of discordant melting and ineffective mixing. In this study, the mixing effect of “twin-wire-one-drop” was analysed, and droplets of different diameters were used for fabricating Ti-48Al walls. It was found that the mixing effect in the droplet was great, but there were still local unmixed areas, and a completely uniform Ti-48Al wall could be obtained by using small droplet mode. Meanwhile, incompletely mixing regions with composition difference greater than 5% appeared in many places on the sides of the Ti-48Al wall in huge droplet mode. A numerical model is established to simulate the mixing process after the droplet enters the molten pool. It is found that the secondary droplets generated in huge droplet mode are the main reason for the element inhomogeneity phenomenon. Therefore, keeping the droplet interval short and uniform is beneficial to the element in situ alloying.
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Data Availability
The data that support the findings of the study are available from the corresponding author, lifang302@sjtu.edu.cn, upon reasonable request.
References
Wu X (2006) Review of alloy and process development of TiAl alloys. Intermetallics 14:1114–1122. https://doi.org/10.1016/j.intermet.2005.10.019
Zhang X, Chen Y, Hu J (2018) Recent advances in the development of aerospace materials. Prog Aerosp Sci 97:22–34. https://doi.org/10.1016/j.paerosci.2018.01.001
Genc O, Unal R (2022) Development of gamma titanium aluminide (γ-TiAl) alloys: a review. J Alloys Compd 167262. https://doi.org/10.1016/j.jallcom.2022.167262
Kothari K, Radhakrishnan R, Wereley NM (2012) Advances in gamma titanium aluminides and their manufacturing techniques. Prog Aerosp Sci 55:1–16. https://doi.org/10.1016/j.paerosci.2012.04.001
Cao L, Wang H, Zou C, Wei Z (2009) Microstructural characterization and micromechanical properties of dual-phase carbide in arc-melted titanium aluminide base alloy with carbon addition. J Alloy Compd 484:816–821. https://doi.org/10.1016/j.jallcom.2009.05.052
Liu J, Liu Y, Zhang Z, Wang H (2022) Parameter optimization and experimental study on tool-vibration-assisted pulsed electrochemical machining of γ-TiAl TNM blades. Appl Sci 12:8042. https://doi.org/10.3390/app12168042
Thomas M, Raviart JL, Popoff F (2005) Cast and PM processing development in gamma aluminides. Intermetallics 13:944–951. https://doi.org/10.1016/j.intermet.2004.12.010
Güther V, Allen M, Klose J, Clemens H (2018) Metallurgical processing of titanium aluminides on industrial scale. Intermetallics 103:12–22. https://doi.org/10.1016/j.intermet.2018.09.006
DebRoy T, Wei H, Zuback J, Mukherjee T, Elmer J, Milewski J, Beese A, Wilson-Heid A, De A, Zhang W (2018) Additive manufacturing of metallic components - process, structure and properties. Prog Mater Sci 92:112–224. https://doi.org/10.1016/j.pmatsci.2017.10.001
Körner C (2016) Additive manufacturing of metallic components by selective electron beam melting—a review. Int Mater Rev 61:361–377. https://doi.org/10.1080/09506608.2016.1176289
Emiralioglu A, Unal R (2022) Additive manufacturing of gamma titanium aluminide alloys: a review. J Mater Sci 57:4441–4466. https://doi.org/10.1007/s10853-022-06896-4
Wu B, Pan Z, Ding D, Cuiuri D, Li H, Xu J, Norrish J (2018) A review of the wire arc additive manufacturing of metals: properties, defects and quality improvement. J Manuf Process 35:127–139. https://doi.org/10.1016/j.jmapro.2018.08.001
Srivastava M, Rathee S, Tiwari A, Dongre M (2023) Wire arc additive manufacturing of metals: a review on processes, materials and their behaviour. Mater Chem Phys 294:126988. https://doi.org/10.1016/j.matchemphys.2022.126988
Ma Y, Cuiuri D, Hoye N, Li H, Pan Z (2014) Effects of wire feed conditions on in situ alloying and additive layer manufacturing of titanium aluminides using gas tungsten arc welding. J Mater Res 29:2066–2071
Ma Y, Cuiuri D, Hoye N, Li H, Pan Z (2014) Characterization of in-situ alloyed and additively manufactured titanium aluminides. Metall and Mater Trans B 45:2299–2303. https://doi.org/10.1007/s11663-014-0144-6
Ma Y, Cuiuri D, Hoye N, Li H, Pan Z (2015) The effect of location on the microstructure and mechanical properties of titanium aluminides produced by additive layer manufacturing using in-situ alloying and gas tungsten arc welding. Mater Sci Eng -Struct Mater Prop Microstruct Process 631:230–240. https://doi.org/10.1016/j.msea.2015.02.051
Duan B, Yang Y, He S, Feng Q, Mao L, Zhang X, Jiao L, Lu X, Chen G, Li C (2022) History and development of γ-TiAl alloys and the effect of alloying elements on their phase transformations. J Alloy Compd 909:164811. https://doi.org/10.1016/j.jallcom.2022.164811
Appel F, Paul JDH, Oehring M (2011) Gamma titanium aluminide alloys: science and technology. John Wiley & Sons
Wang L, Shen C, Zhang Y, Li F, Huang Y, Ding Y, Hua X (2021) Effect of Al content on the microstructure and mechanical properties of γ-TiAl alloy fabricated by twin-wire plasma arc additive manufacturing system. Mater Sci Eng A 826:142008. https://doi.org/10.1016/j.msea.2021.142008
Shen C, Hua X, Li F, Zhang T, Li Y, Zhang Y, Wang L, Ding Y, Zhang P, Lu Q (2021) Composition-induced microcrack defect formation in the twin-wire plasma arc additive manufacturing of binary TiAl alloy: an X-ray computed tomography-based investigation. J Mater Res 36:4974–4985. https://doi.org/10.1557/s43578-021-00412-1
Wang MS, Liu EW, Du YL, Liu TT, Liao WH (2021) Cracking mechanism and a novel strategy to eliminate cracks in TiAl alloy additively manufactured by selective laser melting. Scr Mater 204:114151. https://doi.org/10.1016/j.scriptamat.2021.114151
Cho K, Kawabata H, Hayashi T, Yasuda HY, Nakashima H, Takeyama M, Nakano T (2021) Peculiar microstructural evolution and tensile properties of β-containing γ-TiAl alloys fabricated by electron beam melting, Addit Manuf 46:102091. https://doi.org/10.1016/j.addma.2021.102091
Schwerdtfeger J, Körner C (2014) Selective electron beam melting of Ti–48Al–2Nb–2Cr: microstructure and aluminium loss. Intermetallics 49:29–35. https://doi.org/10.1016/j.intermet.2014.01.004
Tang H, Yang G, Jia W, He W, Lu S, Qian M (2015) Additive manufacturing of a high niobium-containing titanium aluminide alloy by selective electron beam melting. Mater Sci Eng: A 636:103–107. https://doi.org/10.1016/j.msea.2015.03.079
Wartbichler R, Clemens H, Mayer S, Ghibaudo C, Rizza G, Galati M, Iuliano L, Biamino S, Ugues D (2021) On the Formation mechanism of banded microstructures in electron beam melted Ti–48Al–2Cr–2Nb and the design of heat treatments as remedial action. Adv Eng Mater 23:2101199. https://doi.org/10.1002/adem.202101199
Gussone J, Hagedorn Y-C, Gherekhloo H, Kasperovich G, Merzouk T, Hausmann J (2015) Microstructure of γ-titanium aluminide processed by selective laser melting at elevated temperatures. Intermetallics 66:133–140. https://doi.org/10.1016/j.intermet.2015.07.005
Wang J, Pan Z, Cuiuri D, Li H (2019) Phase constituent control and correlated properties of titanium aluminide intermetallic alloys through dual-wire arc additive manufacturing. Mater Lett 242:111–114. https://doi.org/10.1016/j.matlet.2019.01.112
Henckell P, Ali Y, Metz A, Bergmann J, Reimann J (2019) In situ production of titanium aluminides during wire arc additive manufacturing with hot-wire assisted GMAW process. Metals 9(5):578. https://doi.org/10.3390/met9050578
Cai X, Dong B, Yin X, Lin S, Fan C, Yang C (2020) Wire arc additive manufacturing of titanium aluminide alloys using two-wire TOP-TIG welding: processing, microstructures, and mechanical properties. Addit Manuf 35. https://doi.org/10.1016/j.addma.2020.101344
Mohr M, Wunderlich R, Fecht H-J (2022) Thermophysical properties of titanium alloys. In: Metallurgy in Space: Recent Results from ISS. Springer International Publishing, Cham, pp 357–375
Bruno TJ, Haynes WM, Lide DR (2013) (eds) CRC handbook of chemistry and physics: a ready-reference book of chemical and physical data. CRC press
Xin J, Wu D, Shen C, Wang L, Hua X, Ma N, Tashiro S, Tanaka M (2022) Multi-physical modelling of alloy element transportation in wire arc additive manufacturing of a γ-TiAl alloy. Int J Therm Sci 179:107641. https://doi.org/10.1016/j.ijthermalsci.2022.107641
Xin J, Wu D, Chen H, Wang L, Zhou W, Wu K, Zhang Y, Shen C, Hua X, Li F (2023) Effect of droplet transfer mode on composition homogeneity of twin-wire plasma arc additively manufactured titanium aluminide. Int J Adv Manuf Technol 124:1723–1734. https://doi.org/10.1007/s00170-022-10592-7
Wang L, Zhou W, Shen C, Zhang Y, Li F, Ding Y, Xin J, Wang B, Hua X (2022) Effect of substrate temperature on microstructure and mechanical properties of TiAl alloy fabricated using the twin-wire plasma arc additive manufacturing system. J Mater Sci 57:8940–8955. https://doi.org/10.1007/s10853-022-07228-2
Esfahani MRN, Coupland J, Marimuthu S (2015) Numerical simulation of alloy composition in dissimilar laser welding. J Mater Process Technol 224:135–142. https://doi.org/10.1016/j.jmatprotec.2015.05.005
Huang W, Wang H, Rinker T, Tan W (2020) Investigation of metal mixing in laser keyhole welding of dissimilar metals. Mater Des 195:109056. https://doi.org/10.1016/j.matdes.2020.109056
Egry I, Brooks R, Holland-Moritz D, Novakovic R, Matsushita T, Ricci E, Seetharaman S, Wunderlich R, Jarvis D (2007) Thermophysical properties of γ-titanium aluminide: the European IMPRESS project. Int J Thermophys 28:1026–1036. https://doi.org/10.1007/s10765-007-0219-6
Zhou K, Wang H, Chang J, Wei B (2015) Experimental study of surface tension, specific heat and thermal diffusivity of liquid and solid titanium. Chem Phys Lett 639:105–108. https://doi.org/10.1016/j.cplett.2015.09.014
Stone W, Kurfess TR (2007) Grinding titanium aluminide: subsurface damage. Int J Manuf Technol Manage 12:200–224
Sprengel W, Oikawa N, Nakajima H (1996) Single-phase interdiffusion in TiAl. Intermetallics 4:185–189. https://doi.org/10.1016/0966-9795(94)00033-6
Rongy L, Haugen KB, Firoozabadi A (2012) Mixing from Fickian diffusion and natural convection in binary non-equilibrium fluid phases. AIChE J 58:1336–1345. https://doi.org/10.1002/aic.12685
Beckermann C, Viskanta R (1993) Mathematical modeling of transport phenomena during alloy solidification. Appl Mech Rev 46:1–27. https://doi.org/10.1115/1.3120318
Prescott PJ, Incropera FP (1994) Convective transport phenomena and macrosegregation during solidification of a binary metal alloy: I—numerical predictions. J Heat Transfer 116:735–741. https://doi.org/10.1115/1.2910929
DuPont JN, Marder AR (1995) Thermal efficiency of arc welding processes. Weld J 74:406-s
Jiang F, Li C, Chen S (2019) Experimental investigation on heat transfer of different phase in variable polarity plasma arc welding. Weld World 63:1153–1162. https://doi.org/10.1007/s40194-019-00722-3
Wu D, Hua X, Ye D, Li F (2017) Understanding of humping formation and suppression mechanisms using the numerical simulation. Int J Heat Mass Transf 104:634–643
Funding
This work is supported by the Fundamental Research Funds for the Central Universities and Institute of Marine Equipment. And, the authors also gratefully acknowledge financial support from Shanghai Rising-Star Program of Science and Technology Commission of Shanghai Municipality (STCSM, Funding No. 23QA1404700) and the “JSPS International Research Fellow” project (21F31063).
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All authors contributed to the study conception and design. Material preparation, data collection and analysis were performed by JX. The numerical model was completed under the guidance by DW. The first draft of the manuscript was written by JX and all authors commented on previous versions of the manuscript. All authors read and approved the final manuscript.
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Appendix: Governing equations and boundary conditions
Appendix: Governing equations and boundary conditions
1.1 Governing equations
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(1)
Species (Ti and Al) conservation equation:
$$\frac{\partial\left(\rho\varphi\right)}{\partial t}+\nabla\bullet\left(\rho v\varphi\right)=\varphi_s$$(A1)where ρ is the fluid density, which is substituted by the density of Ti-48Al in this model, φ is the weight percentage of alloy element. t is the time, v is a velocity vector, and φs is an alloy element source term caused by droplets. To save computing consumption, only φAl was calculated. As discussed in Sect. 3.1, the droplets enter the molten pool at intervals of 1.8 s or 0.225 s, respectively. The droplets are set to be positively spherical, and φAl of the 20% volume above the sphere is set to be 100% Al, φAl of the 80% volume below the sphere is set to be 39.11%, when φAl of the existing parts is set to be 48%. The difference between the Al content of the molten drop and the molten pool will cause the change of the distribution of Al content in the molten pool.
According to Fick’s law, the diffusion behaviour of metal atoms in an alloy satisfies the following formula:
$$J= -D\bullet \frac{dc}{dx}$$(A2)Sprengel et al. [40] measured interdiffusion in TiAl around the stoichiometry in single-phase couples Ti50Al50, given a D value at about 10−12 m2/s. Given the assumption that the edge of the molten pool is 2 mm away from the molten pool center, and the average velocity in the molten pool is about 0.1 m/s, we can use Peclet number (Pe) to estimate the convective effect and diffusive effect.
$${P}_{e}= \frac{{N}_{conv}}{{N}_{diff}}=\frac{LU}{D}\approx \frac{2\times {10}^{-3}\bullet 0.1}{{10}^{-12} }=2\times {10}^{8}$$(A3)Therefore, it is verified that the convective effect is several orders of magnitude larger than the diffusive effect [41], and the mentioned element inhomogeneity is mainly caused by macroscopic movement of liquid metal phases, so that the diffusive effect of alloy elements was ignored in our model [42, 43].
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(2)
Mass conservation equation
$$\frac{\partial \rho }{\partial t}+\nabla \bullet \left(\rho v\right)={m}_{s}$$(A4)where ms is a mass source term mainly caused by droplets. Generally speaking, the increase in the mass of the entire computing domain is equal to the amount of wire feed feeding, that is, 18.6 mm3/s. Under different conditions, the droplets enter the molten pool at different frequencies, resulting in mass changes in the conservation equation. The movement of the existing workpiece also causes a change in mass. However, the volume entering the calculation domain is the same as the volume leaving the calculation domain, so the mass change of the calculation domain is mainly caused by the droplet.
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(3)
Momentum conservation equation
$$\frac{\partial \left(\rho v\right)}{\partial t}+\nabla \bullet \left(\rho vv\right)=-\nabla P+\nabla \bullet \tau +{m}_{s}v+{f}_{b}$$(A5)where P is the pressure, τ is a viscosity stress tensor, and fb is the body force, which is referred to as gravity in this model. The gravity field is distributed along the negative Z-axis with a value of 9.8 m/s2.
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(4)
Energy conservation equation:
$$\frac{\partial \left(\rho h\right)}{\partial t}+\nabla \bullet \left(\rho vh\right)=\nabla \bullet \left(K\nabla T\right)+{h}_{s}$$(A6)where h is the enthalpy, K is the thermal conductivity, T is the temperature, and hs is an energy source. During the wire feeding process, the wires are heated and melted by the plasma arc, transferring energy to the molten pool. The droplets are set to appear at a temperature of 2200 K and enter the molten pool. During the simulation process, the upper surface of the liquid phase is always heated by the arc, and the distribution of the arc heat is discussed in detail in the following section.
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(5)
VOF equation:
$$\frac{\partial F}{\partial t}+\nabla \bullet \left(\rho vF\right)={F}_{s}$$(A7)where F is the volume fraction of the fluid in a cell and \({F}_{s}\) is a volume fraction source term caused by designed droplet.
1.2 Boundary conditions
The plasma arc heat input acted on the free surface was modelled as a fixed double-ellipse density function. The heat conduction and radiation were also applied on the free surface, while the evaporation heat loss is ignored owing to the low molten pool temperature. Considering that the arc heat was not applied to a flat workpiece, but to an existing wall with a certain shape, the height of the free surface was read and transformed in this model.
where ηq is the plasma arc energy efficiency; Uq is the plasma arc voltage; Iq is the plasma arc current; σqx, σqy, and σqz are effective radii of the plasma arc heat in x, y, z directions; hc is the heat transfer coefficient; T0 is the ambient temperature (873 K); σ is the Stefan-Boltzmann constant; and ε is the surface emissivity. Specifically, σqr and σqf represent the distribution coefficients of the double ellipsoid model in the positive direction and the negative direction. hx,y represents the z coordinate of the highest point of the molten pool at the same x and y coordinate position at this time. Due to the curved surface of the molten pool in the upper deposition, the z coordinate of the calculation element is deformed in this model, and the z coordinate value z′ is re-assigned according to its proportion to the current height of the molten pool surface.
Previous studies showed that the plasma arc energy efficiency was only 47 ~ 66% [44, 45]. Given that droplet formation takes up a portion of the arc energy, the plasma arc energy efficiency of 50% is adopted, which is lower than usual value.
The balance of plasma arc pressure and surface tension pressure on the free surface is expressed as:
where μ is the fluid viscosity, vn is a normal velocity vector, n is a surface normal vector, Parc is the plasma arc pressure, R is the radius of the surface curvature, γ0 is the surface tension of the fluid at the melting point, and Tm is the melting point.
The plasma arc pressure is approximated as a fixed gaussian distribution density function:
Pmax is the maximum plasma arc pressure and σp is the effective radii of the plasma arc pressure. The values are calculated and adjusted according to previous research [46] and high-speed camera records, where σp is 0.00351 and Pmax is 600.
The Marangoni shear stress caused by the temperature gradient is applied on the free surface in the tangential direction:
where μ is the fluid viscosity, exhibited in Fig. 3d, vt is a tangential velocity vector, and S is a tangential vector.
The velocity is set as − 0.9 m/s at the x direction boundary. The value of φAl is also set as 0.3422 (48% in atomic ratio) on the wall boundary for initiation.
The details of the iteration scheme for numerically solving the governing equations with required equations can be found in our previous work [32, 46].
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Xin, J., Li, F., Wu, D. et al. The mechanism of element inhomogeneity in TW-DED-arc fabricated γ-TiAl alloy. Weld World 68, 953–968 (2024). https://doi.org/10.1007/s40194-024-01697-6
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DOI: https://doi.org/10.1007/s40194-024-01697-6