Effect of Ti2AlC Addition on the Microstructure and Mechanical Property of Additive Manufactured Inconel 718 Alloys via Laser Powder Bed Fusion

doi:10.1007/s40195-025-01877-3

Abstract

Abstract:

Improving the high-temperature performance of Inconel 718 (IN718) alloys manufactured via laser powder bed fusion (LPBF) has been the most concerned issue in the industry. In this study, the effects of Ti₂AlC inoculants on microstructures and high-temperature mechanical properties of the as-built IN718 composites were investigated. According to statistical results of relative density and unmelted particle area in as-built alloys, the optimal energy of 112 J/mm³ was determined. It was observed that the precipitation of the MC carbide was significantly enhanced with the addition of Ti₂AlC, restricting the precipitation of the Laves phase. The MC particles were uniformly distributed along the subgrain boundaries, which contributed to the dispersion strengthening. Meanwhile, the MC particles served as nucleation sites for heterogeneous nucleation during the solidification process, facilitating the refinement of columnar and cellular grains. The simulated Scheil-Gulliver curves showed that the precipitation sequence of phases did not change with Ti₂AlC inoculants. The as-built 1%Ti₂AlC/IN718 sample demonstrated an ultimate tensile strength of 998.78 MPa and an elongation of 18.04% at 650 °C, revealing a markedly improved mechanical performance compared with the LPBF-manufactured IN718 alloys. The high-temperature tensile strength of 1%Ti₂AlC/IN718 sample increased to 1197.99 MPa by heat treatment. It was suggested that dislocation strengthening and ordered strengthening were two most important reinforcement mechanisms.

Key words: IN718 alloy, Laser powder bed fusion, Ti₂AlC inoculants, Heat treatment, High-temperature property

Huihui Wang, Qianying Guo, Chong Li, Lei Cui, Yiming Huang, Yongchang Liu. Effect of Ti₂AlC Addition on the Microstructure and Mechanical Property of Additive Manufactured Inconel 718 Alloys via Laser Powder Bed Fusion[J]. Acta Metallurgica Sinica (English Letters), 2025, 38(9): 1481-1498.

Figures/Tables 20

Table 1 Chemical compositions of IN718 and Ti2AlC/IN718 powder (wt%)

Sample	Ni	Cr	Nb	Mo	Al	Ti	Co	Cu	C	Fe
IN718	50.74	19.40	5.03	3.10	0.46	0.88	0.13	0.03	0.03	Bal.
0.5%Ti₂AlC/IN718	50.49	19.30	5.00	3.08	0.56	1.28	0.13	0.03	0.07	Bal.
1%Ti₂AlC/IN718	50.23	19.21	4.98	3.07	0.66	1.57	0.13	0.03	0.12	Bal.

Fig. 1 a, b SEM images of Ti2AlC/IN718 composite powder, c crystal structure of Ti2AlC

Fig. 2 Schematic diagrams of a LPBF process, b dimensions of specimens for the microstructure observation and tensile test

Table 2 LPBF process parameters

Laser power, $P{ }$ (W)	Scanning speed, $v$ (mm/s)	Hatch distance, h (${\mu}\, \text{m}$)	Layer thickness, t (${\mu}\, \text{m}$)
22-365 at 20 intervals	850-1250 at 100 intervals	80	40

Fig. 3 LPBF results of Ti2AlC/IN718 alloys: a microstructures, b relative density, c unmelted particle area

Fig. 4 SEM images and 3D CT detection results of different as-built samples: a IN718, b IN718 + 0.5%Ti2AlC, c IN718 + 1%Ti2AlC

Fig. 5 EBSD results of the as-built IN718, 0.5%Ti2AlC/IN718 and 1%Ti2AlC/IN718 samples: a-c grain boundary, d-f inverse pole figure, g-i pole figure

Fig. 6 TEM images of columnar and cellular substructures in the as-built samples: a-c IN718 sample, d-f 1%Ti2AlC/IN718 sample

Fig. 7 SEM images of the as-built IN718, 0.5%Ti2AlC/IN718 and 1%Ti2AlC/IN718 samples: a-c molten pool morphology, d-f pass-pass morphology, g-i layer-layer morphology

Fig. 8 EPMA mapping images of segregations for different regions of the as-built 1%Ti2AlC/IN718 samples: the regions near a layer-layer MPB, b pass-pass MPB, c inside the cellular structure

Fig. 9 TEM results of as-built samples: a-c IN718 sample, d-f 1%Ti2AlC/IN718 sample

Fig. 10 SEM and statistical results of as-built alloys and precipitated phase after heat treatment: a, d IN718, b, e 0.5%Ti2AlC/IN718, c, f 1%Ti2AlC/IN718 samples

Fig. 11 IPF maps, KAM maps and grain boundary maps of a-c IN718, d-f 0.5%Ti2AlC/IN718, g-i 1%Ti2AlC/IN718 samples on X-Z plane after heat treatment

Fig. 12 TEM bright-field image, dark-field image and size distribution of substructure after heat treatment: a, d, g IN718, b, e, h 0.5%Ti2AlC/IN718, c, f, i 1%Ti2AlC/IN718 samples

Fig. 13 High-temperature tensile stress-strain curves of a as-printed samples, b as-built samples after heat treatment

Fig. 14 SEM images taken from fracture surfaces of: a, b as-built IN718 sample, c, d at-built 1%Ti2AlC/IN718 sample

Fig. 15 Scheil-Gulliver curves for nonequilibrium solidification process of a IN718, b 0.5%Ti2AlC/IN718, c 1%Ti2AlC/IN718, d initial precipitation temperature of three phases

Fig. 16 Schematic diagram of the solidification evolution of IN718 and 1%Ti2AlC/IN718

Table 3 Contribution to total yield strength by Ti2AlC

No.	$d_{{\text{G}}}$ (μm)	$d_{{\text{C}}}$ (nm)	$d_{{\text{P}}}$ (nm)	$V_{{\text{P}}}$ (%)	$\Delta \sigma_{{{\text{GB}}}}$ (MPa)	$\Delta \sigma_{{\text{D}}}$ (MPa)	$\Delta \sigma_{{\text{P}}}$ (MPa)
IN718	30.8	478	476	0.48	-	-	-
0.5%Ti₂AlC/IN718	28.7	438	178	0.23	3.82	27.07	6.75
1%Ti₂AlC/IN718	23.7	403	97	0.11	14.88	55.16	9.15

Table 4 Contribution to total yield strength by heat treatment

No.	$d_{{\text{G}}} $ (μm)	$d_{{\text{P}}} $ (nm)	${\lambda }$ (nm)	$f_{{\gamma^{\prime\prime}}}$	$R_{{\gamma^{\prime\prime}}} $ (nm)	$f_{{\gamma^{\prime}}}$	$R_{{\gamma^{\prime}}}$ (nm)	$\Delta \sigma_{{{\text{GB}}}} $ (MPa)	$\Delta \tau$($\gamma^{\prime }$) (MPa)	$\Delta \tau$($\gamma^{\prime \prime }$) (MPa)	$\Delta \sigma_{{\text{P}}}$ (MPa)
IN718	42.5	683	9124	0.077	9.55	0.015	6.9	-	-	-	-
0.5%Ti₂AlC/IN718	34.5	720	5437	0.083	8.96	0.056	8.12	9.95	80.19	0.1	4.36
1%Ti₂AlC/IN718	27.1	794	4586	0.101	11.23	0.079	9.4	22.84	122.58	47.2	6.51

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Effect of Ti₂AlC Addition on the Microstructure and Mechanical Property of Additive Manufactured Inconel 718 Alloys via Laser Powder Bed Fusion

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