Volume 5 - Year 2018 - Pages 90-99

DOI:

### Selective Laser Melting of Metal Powders in Additive Manufacturing

Tsung-Wen Tsai^{1}, Wai-Kwuen Choong^{1}, Wei-Chin Huang^{1}, Chuan-Sheng Chuang^{1}, De-Yau, Lin^{1}, Sung-Ho Liu^{1}, Ji-Bin Horng^{1}, Jinn-Kuen Chen^{2}

^{1}Laser and Additive Manufacturing Technology Center, Industrial Technology Research Institute

No. 8, Gongyan Rd., Liujia District, Tainan County, Taiwan 734

matttsai@itri.org.tw; Horus-Huang@itri.org.tw; CS_Zhuang@itri.org.tw; dylin@itri.org.tw; RiverLiu@itri.org.tw;

jibin@itri.org.tw

^{2}Department of Mechanical and Aerospace Engineering, University of Missouri

Columbia, MO, U.S.A. 65211

chenjnk@missouri.edu

**Abstract** - * Fundamental mechanisms of selective laser melting (SLM)
of metal powders in additive manufacturing (AM) were investigated numerically and experimentally.
A simplified 2D finite element model of multiphase fields was proposed to simulate the SLM process
based on the conservation equations of mass, momentum and energy. Multiple dynamic physics/
phenomena considered in this work include heat transfer, solid/liquid and liquid/vapor phase
changes, vapor pressure, surface tension, gravity, melt flow, gas flow, wetting and bonding
of powder particles with the melt, and re-solidification. To deposit laser energy to the
powder bed, the liquid/gas interface was tracked using a level set method. The numerical
simulation was carried out using COMSOL Multyphysics®. To validate the proposed methodologies,
an SLM experiment was performed for Ti6Al4V powders. It was shown that the simulation results
of the cross-section shapes and the heights of re-solidified parts are in good agreement with
the experimental measurements.
*

** Keywords:** Selective Laser Melting, Multiphysics Modeling, Level Set Method.

© Copyright 2018 Authors - This is an Open Access article published under the Creative Commons Attribution License terms Creative Commons Attribution License terms. Unrestricted use, distribution, and reproduction in any medium are permitted, provided the original work is properly cited.

Date Received: 2017-09-08

Date Accepted: 2018-08-10

Date Published: 2018-XX-XX

#### 1. Introduction

Additive manufacturing (AM) has become a critical technology in many industry sectors, particularly in the past decade [1-4]. For most of AM processes of metal powders, selective laser melting (SLM) plays an important role in building complex-shaped parts by selectively melting powders layer-by-layer. Each time of laser scanning, those powders in the powder bed are selectively heated and melted, the melt flows, coalesces, and forms a narrow melt track. After the laser beam moves away, the localized melt pool rapidly cools down and re-solidifies. The consolidation of the melted part of metal powders forms a solid layer. Thus, a 3D part can be fabricated by continuously feeding of powders layer by layer with the SLM in an intended AM process. The quality of an AM product strongly depends on material, powder arrangement, laser processing parameters, and scanning scheme.

#### 2. Related Work

Due to the highly localized heating and layer-by-layer melting nature, temperature gradients in a heated spot and its surrounding region are very high. Residual deformation and thermal stress hence are induced after rapidly cooled down from the melting temperature [5-7]. As a result, a manufactured part could severely be distorted, cracked, or even raptured. In some cases, an AM product must be discarded on site because of these undesired detriments [8-10]. It is particularly true for the AM of metal and ceramic powders. Another defect is the “undesired” porosities produced inside a 3D part due to imperfect powder particle packing and/or improper SLM processing [11].

When a powder starts to melt from the upper surface, the molten metal flows down along its surface mainly driven by gravity and surface tension, wets and bonds with the neighbor powders, and fills the air gap among powders. The re-solidified part may not be fully dense if the SLM process is not properly controlled and no additional means, such as pressure, is applied. The residual deformation, thermal stress, and defects produced after an AM process dictate material properties and the quality of the end product. Therefore, there is a need for optimizing the SLM processing parameters in order to make AM products of high quality. This requires a thorough understanding of the fundamental physics involved in the SLM process and the mechanisms of defects formation and evolution during the AM process.

To guide the AM efforts to produce a high quality product, a great number of experiments [11-16] and theoretical studies [7, 17-24] have been dedicated to optimizing the SLM process, particularly for how to reduce residual thermal stress and porosities. It is difficult to experimentally observe the dynamic evolution of powders in such a highly localized, small volume during and aftermath of the laser-material interaction. Thus, understanding of defects formation (shape, size, location and number of voids) and residual thermal stress generation becomes unviable. Because of that, the laser process parameters and scanning schemes usually are attained through trial-and error, which is cost expensive and time consuming. This drawback makes modelling and simulation more versatile, though there are numerous challenges to be overcome.

Modelling and simulation of a metal powder bed
AM process is quite complicated. It is a line-by-line and then layer-by-layer
process of a tremendously huge number of powder particles. Moreover, the
physical phenomena involved in the process are quite complex [19, 20], including
laser energy deposition on dynamic powder surfaces, melting of solid powders,
diffusive and radiative heat transfer in solid powders and in the molten parts,
capillary effects, gravity, melt motion, wetting and bonding with other powders,
consolidation of the liquid pool, solid-state transformation, grain coarsening,
residual thermal stress, etc. Among which, the melt pool generated by scanning
laser beam and its subsequent melt motion is highly dynamic [19-21], mainly
governed by gravity and surface tension with low viscosity of liquid metal. Indeed,
an AM process of metal powders is a transient, multiscale and multiphysics
problem. According to Sames et al. [25], it comprises (1) a micro-scale (10^{-9}
m to 10^{-6} m) for solidification, solid-state transformation, grain
coarsening, etc., (2) particle scale (10^{-6} m to 10^{-3} m)
for laser-powder interaction and powder consolidation, (3) meso-scale (~10^{-3}
m) for phase change dynamics, fluid motion, re-solidification, etc., and (4)
macro scale (10^{-3} m to 1 m) for shape distortion, residual stress,
etc. For such a complicated problem, a truly predictive simulation for the
entire AM process that spans a large range of length and timescales could be
extremely difficult, if not impossible. For example, it may take decades of
computational time on a large cluster to run a simulation of ~10^{12}
metal particles and ~10^{9} m laser scanning path for a typical volume
of 1 m^{3} processed by laser irradiation of a few minutes [25]. To
address this hopeless challenge, a great effort has been ongoing in academia,
industry, and national laboratories to leverage existing integrated
computational materials engineering tools. An overview of the modelling and
simulation activities on AM can be found in Sames et al. [25]. The reviews of
finite element methods which are the most popular numerical method used for
simulating AM process were given by Schoinochoritis, et al. [26] and King, et al. [27].

Although a great deal of knowledge and techniques has been acquired to date, understanding of the fundamental physics and control of laser-powder interaction and formation and evolution of defects is still not thorough, if not in the infant stage. In this work, a transient, 2D finite element model is proposed to investigate laser heating of metal powders and the subsequent process that turns into a solid part. Three conservation equations of mass, momentum and energy, together with laser-powder heating, solid/liquid and liquid/vapor phase changes, melt motion and filling air gap among powders, wetting and bonding with neighbor powders, consolidation of molten metal part, and formation of the solid part, are solved simultaneously using COMSOL Multiphysics®. To deposit laser energy to the surface of powder bed, the liquid/gas interface is tracked using a level set method. Laser heating experiments are performed for Ti6Al4V powders. The proposed methodologies and numerical simulations are validated against the experiment measurements by comparing the cross-section shapes and the heights of the re-solidified parts.

#### 3. Mathematical Modelling

Consider a single line scanning of
continuous-wave (CW) laser on a layer of spherical Ti6Al4V powders placed on a
titanium substrate. The laser beam of power (P) moves in the z-direction at a
constant speed (v_{s}). Because the process result is independent of z,
except for the regions near the two ends, the final cross-section profile of
the SLM part at a location z can be simulated with a simplified 2D model I
shown in Fig. 1(a), in which one and a half powders are considered in the
x-direction and the symmetric conditions are imposed at x = 0.

For a consecutive line-by-line scanning, the process result is, except for the region near the surrounding boundary of the substrate, independent of x and z after the entire xz plane is scanned. Thus, the cross-section profile of the SLM part at a location x can be simulated using another simplified 2D model II shown in Fig. 1(b). For simplicity, only seven powders are considered here. In both models, the sizes of and distance between powder particles are arranged based on the normal packing of powder feedstock in a layer SLM process [25]. The analysed domains other than the powders and substrate are argon gas.

3.1. Level Set Function

When laser light impinges onto a material, the laser energy will be absorbed, depending on the value of material optical absorptivity. In this study, the laser energy absorption by the argon gas is not considered. Due to the fact that the optical penetration depth of metals is on the order of tens nanometers, about three orders smaller than the sizes of Ti6Al4V powders, it is reasonable to assume that the laser energy is only deposited on the surfaces of powder material. Once the powders absorb the laser energy, the temperature in the heated subsurface layer rapidly increases and then the thermal energy conducts into the surrounding region. Those parts of the powders will undergo a solid/liquid phase change when their temperature reaches the melting point and the liquid/vapor phase change when the temperature of liquid reaches the boiling point. The melt will flow down along the powder surface, wet with the adjacent powders, and consolidate. The dynamic outer contour of the melt must be traced since the laser energy will be deposited onto the surfaces of the melt (and the solid powders) that are directly exposed to the laser beam. In this work, the liquid/gas interface is tracked using a level set method [28, 29]:

where *f* is the level set function,
is the velocity of fluid mixture in the thin
layer of interface of thickness *e*, and g is the speed
of re-initialization. The value of *f* is set to be one (1) in the argon gas region
and -1 in the region of liquid, and smoothly varies from 1 to -1 over the layer
of mixture. The interface is determined by the zero-level set of the function *f*. The
interface velocity in the above equation is expressed as [30]:

where is the normal vector of the interface, and is the local mass flux of evaporation described by

in which* m *is atomic
weight of the liquid, *k _{b}* Boltzmann constant,

*p*saturated vapor pressure,

_{sat}*T*is temperature, and β

*the retrodiffusion coefficient which is assumed to be zero in this work. The saturated vapor pressure in Eq. (3) is given as:*

_{r}where* p _{o}*
is 101,325 Pa,

*L*is the latent heat of evaporation, and

_{v}*T*is the boiling point.

_{vap}3.2. Governing Equations

Depending on the occurrence of melting and vaporization, three phases of solid, liquid and vapor could appear in an SLM process. The responses of the three phases are different and should be solved using different models. Nevertheless, the physics of each phase can be described by the conservation equations of mass, momentum and energy though the forms are different. By removing the unneeded equations and/or terms from the three equations for a particular phase, a general mathematical model of heat transfer and fluid dynamics can be expressed as follows [31-36]:

In
the above equations, r is mass density, *p* pressure, *I*
identity matrix, m dynamic viscosity, (.)* ^{T}* transposed matrix, gravity, g surface tension
coefficient, surface normal vector, k surface
curvature, d(f) delta
function of the level set value,

*c*specific heat, T temperature, and k thermal conductivity. The Marangoni effect is neglected here, and the surface tension coefficient is assumed to be constant. For simplicity, the solid/liquid phase transformation is modelled by including the latent heat of fusion to the heat capacity of the powders. The thermal properties of the mixture in the thin layer of interface vary smoothly over the thickness by assuming the following relations:

_{p}where *v _{f}*
= (1+

*f*)/2 is the volume fraction of the liquid. The normal vector and curvature of the interface in Eq. (6) can be determined from the level set function

Since
the laser energy is assumed to be absorbed only at the surfaces of melted and
un-melted powders, the laser heat flux *q _{laser }*for the 2D model
I in Fig. 1(a) is derived from a line-scanning Gaussian laser beam

where*
R* is the surface reflectivity; *r*_{o} is the radius of laser
spot on the powder bed. For the 2D model II in Fig. 1(b), the moving laser heat
flux is given as:

The thermal boundary condition at the interfaces between the solid powders and gas and between the melted metal and gas that includes laser energy flux, heat loss due to vaporization from the melted powder(s) if occurs, and the heat loss from radiation and convection becomes

where σ denotes the
Stefan-Boltzmann’s constant, *h _{c}* is the heat transfer
coefficient, and

*T*

_{∞}is the surrounding temperature. The energy loss

*q*from vaporization is estimated using the recondensation rate in the Knudsen jump [37].

_{evap}In the beginning of
laser process, the powders are solid. They could be melted partially or
completely, and a small amount of material could be vaporized. In the numerical
analysis of the solid part of powders, the convection term in the heat
conduction equation (7) is removed and the mass continuity equation (5) and
Navier-Stokes equations (6) are not needed. For the argon gas, the terms of thermal
expansion and surface tension on the right-hand side of Eq. (6) are dropped off.
The geometric level set method is mainly used to track the liquid-gas
interface. The movement of the interface is realized by advecting the *f* variable
using the velocity field calculation. Across the interface, the *f* varies
progressively with a smooth step function, in addition to the properties
variation** **from a phase to the other. The aforementioned heat transfer
equation, the fluid partial differential equations, and the level set equation
are simultaneously solved using the fully coupled solver in *COMSOL
Multyphysics®.*

#### 4. Experiment

To validate the simulation results, an SLM
experiment was performed to measure the cross-section shapes and
the heights of the re-solidified parts. The Ti6Al4V powders of average diameter
30 μm with purity exceeding 99.95% were spread on a titanium substrate. The
experiment was carried out with the EOSINT M270 laser melting machine. The
source of radiation is a CW fiber laser of maximum power 200 W, wavelength
1,070 nm, and spot size (*r _{o}*) 35 μm. The maximum laser
scanning speed can be up to 7.0 m/s. In this experiment, a single fusion line
was produced by the laser beam at power 175 W. Three scanning speeds of 1,650 mm/s,
1,250 mm/s and 850 mm/s were tested. The re-solidified profile
of the molten track was measured with a 3D optical profiler (Plu 2300,
Sensofar). The experiment was conducted at the Laser and Additive Manufacturing
Technology Center, ITRI.

#### 5. Results and Discussions

In the numerical analysis, the parameters of
material and laser beam are the same as those used in the experiment. The properties of
Ti6Al4V powders can be found in Boyer et al. [34]. The
properties of argon gas are: density () = 0.1 kg.m^{-3}, viscosity () = 510^{-4 }Pa.s, heat capacity (*C _{P}*

_{gas}) = 520 J.kg

^{-1}K

^{-1}, and thermal conductivity (

*k*) = 0.017 W.m

_{gas}^{-1}K

^{-1 }[38]. Other properties used in the simulation are:

*e*=

*1*

*10*,

^{-6}*g*= 1 m/s ,

*R*= 0.55 , and

*h*=100 W/(m

_{c}^{2}.K) . The convergence test was carried out with three different finite element meshes for the case of

**Model I with the laser scanning speed of 1,250 mm/s. >In the following simulations, the numbers of elements used are 9,605 for a powder and 6,036 for argon gas in the Model I, and 17,168 for each powder and 5,952 for argon gas in the Model II. A backward, adaptive time-stepping algorithm is employed to implement the time integration. The initial and maximum timesteps are set at 1 ps and 1 ms respectively for the momentum and energy equations. The accuracy tolerance is controlled within 0.01%.**

Figure 2 shows temporal
evolution of the isotherm and geometry profile simulated for the model I,
including melting of the metal powders, phase transformation from solid to
liquid, melt flow, and re-solidification of the liquid phase. The laser
scanning speed studied here is 1,250 mm/s. At *t* = 34
μs, the peak temperature has already exceeded the melting point (1,923 K).
The central powder begins to melt from the top surface and soon lose its
spherical shape (e.g., at 48 μs) because the gravity and surface tension
act immediately to pull the newly liquefied material into the melt flow. After
the melt of the central powder touches the boundaries of the melt of the
central powder touches the boundaries of the two side powders, formation and
dynamics of the melt pool can be observed (56 μs – 97 μs). All the
powders achieve full melting at about 68 μs and then consolidate and
finally form a semi-circular cylinder at about 97 μs. The effects of
surface tension and gravity on the melt motion are manifest during this period
of time. The maximum temperature in the field is found to be 4,152 K (the
boiling point) shown at 56 μs and decreases to room temperature at about
2000 μs. It is interested in noting the different cross-section profiles
at 56 μs and 2000 μs.

The vector distribution
of velocity in the melt pool is shown in Fig. 3. The molten portion of the
central powder accelerates downward by gravity and reaches the highest speed of
about 7.26 m/s at 48 μs. After the melt reaches the the side powders, a
great amount of the melt is quickly pulled, via surface tension, by the
neighbor powders, leading to a bowl-shaped surface of the melt track. The
gravity thus forces the melt to flow backward (*t* = 56 μs) and
eventually form, together with the two completely molten side powders, a melt
track of cylinder-like shape at about *t* = 97 μs.

The evolution of the melt track is exhibited
by the velocity vectors in Figs. 3(d)-3(g). The shape of the
re-solidified part is displayed in Fig. 3(h) at *t* = 2000 ms. At this
time, the velocity of the melt is almost zero since it is cooled to room
temperature (Fig. 2(h)). It is noted that the small white spots shown in the
figures are voids of gas.

Figure 4 compares the experimental and numerical results of the final parts made by the three scanning speeds (1,650 mm/s, 1,250 mm/s and 850 mm/s). For the case of scanning speed 1,650 mm/s, the two side powders only melt in the region facing to the central one. The cross-section profile is quite different from the other two cases. However, the present simulations agree fairly well with the experimental results for the cases of the two slower scanning speeds. The simulated height and width are about 31.1 μm and 90 μm versus the experimental measurements 35.5 μm and 111.3 μm respectively for the scanning speed 1,250 mm/s, and about 30.8 μm and 100 μm versus 26.8 μm and 131 μm respectively for the 850 mm/s. No porosity is present in the consolidated parts. It is noted that due to the uncertainty of the laser and material parameters, the experimentally measured width and height of cross section of the melt pool could vary at different cross sections that are produced by laser scanning.

The balling effect was experimentally observed and explained by the Plateau-Rayleigh capillary instability of the melt pool [3, 39]. The result shown in Fig. 5 simulated with the scanning speed 2,050 mm/s may suggest the occurrence of balling. It is very likely that the final part could break into three separate pieces of powder size, similar to the experimental result shown in Fig. 4(a).

The conjectured breakages respectively start from the tops of the sizable voids and extend to the top surface of the part, caused by the intensified residual thermal stress in these regions during or after cooled down. This conjecture needs further stress and fracture analysis. The balling effect simulated here is due to insufficient time for the trapped air to escape out of the melt pool, not due to the Rayliegh instability. The undesired defects resulting from the balling include high surface roughness, discontinuous scan tracks, and/or broken parts. The ways to avoid balling are to (1) deposit sufficient laser energy by either increasing laser power or decreasing the scanning speed and/or (2) properly pack a dense powder bed. The improvement by decreasing the laser scanning speed is demonstrated as the results shown in Figs. 4(b) and 4(c).

For the
model II,
the simulated dynamic formation of the melt track is shown in Fig. 6, where the
laser scanning speed is 1,250 mm/s. The laser beam is initially focused at *z*
= 0, i.e., the tip-top of the second powder from left, moves to the right, and
finally stops at the tip-top of the sixth powder. At *t* = 20 μs, the
laser beam has travelled over 25 μm. The second powder is
completely melted and the third one is under melting at this time. The melt of
the second powder has arrived at and adhered to the two adjacent powders (see
Figs. 6(a)). It can be seen from Fig. 6(b) that the velocity vectors point away
from the focused area of the laser beam. The velocity of the backward melt flow
is higher than that of the forward flow since less material is molten ahead.
This strong backward flow drives the melt up and along the right surface of the
first powder. Apparently, a portion of the first powder also melt. According to Korner, et
al. [21],
the molten particles would be ejected vertically and backward if surface
tension is ignored. In contrast, Fig. 6 shows here that with surface tension
the newly molten portion merges almost immediately into the melt flow.At *t* =
100 ms, five
powders have completely melted, see Figs. 6(c) and 6(d).

The
surface tension effect can be seen from the adhesion of the melt and formation of
the smooth top surface. At *t* = 100~200 s, the melt
on the top pool flows leftward while the melt in the bottom flows rightward (Figs.
6(d) & (f)). The resulting large contact area with the substrate leads to a
faster heat transfer that makes cooling down of the melt track faster than that
no surface tension is acting [27].

The simulated consolidated track at *t* = 2000
s can be seen
in Figs. 6(g) and 6(h), where the melt cools down to room temperature. The
average height of the final part is about ∼20m, which is in a good correlation with the data [27]. Generally
speaking, the compact layer has a realistic height of around 67% of the powder
layer as observed in experiment and estimated from the powder packing density.
Unlike the simulation result shown in Fig. 4, no air void is simulated for this
scanning speed except the one close to the first powder.

#### 5. Conclusions

A 2D finite element model of multiphase fields is proposed to investigate the SLM of metal powders for AM, based on the conservation equations of mass, momentum and energy, along with multiple physics of solid/liquid and liquid/vapor phase changes, vapor pressure, gravity, surface tension, melt motion, wetting of powder particles with melt, and re-solidification. To deposit the laser energy, the liquid/gas interface is tracked using a level set method. All the equation and physics are coupled and solved simultaneously in COMSOL Multyphysics®. The simulations of the cross-section shapes of the re-solidified parts by a single line laser scanning and the heights of a single layer by adjacent line-by-line laser scanning are compared with the experimental measurements for Ti6Al4V powders. The present simulation clearly shows that air voids in a re-solidified parts can be removed by slowing down the laser beam scanning speed. In addition, the good correlations of the present two models with the experiments suggest that the present approach can achieve realistic results for the SLM process of metal powders. Further investigation of residual deformation and thermal stress induced in an AM part is suggested.

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