Novel Hybrid Manufacturing Process of CM247LC and Multi-Material Blisks

The study on CM247LC used the traditional approach for Near-Netshape Hot Isostatic Pressing (NNSHIP) with sacrificial low carbon steel tooling, which was built using Selective Laser Melting (SLM), to produce a shaped CM247LC blisk. The assessment of the microstructure focused on both the exterior components in order to determine the depth of the Fe-diffusion layer and on the interior microstructure. Samples were extracted from the Hot Isostatic Pressed (HIPped) components for tensile testing at both room and elevated temperatures. The components were scanned to assess the geometrical shrinkages due to Hot Isostatic Pressing (HIPping). An oversized blisk was also produced based on the measurements as a demonstrator component. In addition, a further study was carried out on a novel idea that used a solid IN718 disk in the centre of the blisk to create a multi-material component.


Introduction
Additive Manufacturing (AM), as a netshape technology, has developed rapidly in the past 10 years. Recent interest in the processing of more expensive materials has been driven by the ability of the technique to potentially reduce material waste [1][2][3][4]. Selective Laser Melting (SLM) is an AM process that uses a high intensity laser to selectively melt defined areas geometries layer by layer and therefore allows the production of near netshape components directly from the metal powder [5][6][7][8][9].
CM247LC is a chemically modified version of the more common MAR M247. Table 1 shows the chemical composition of CM247LC, which was designed with a low C-content [3]. Furthermore, the improved performance of CM247LC is due to the modified elements from MAR M247 [10][11][12]. Therefore, the castability, alloy ductility, fatigue strength and carbide stability of CM247LC DS have been improved compared with MAR M247 [13]. Furthermore, CM247LC DS samples possess the highest tensile strength at a various range of temperatures compared with IN6203 DS and IN792 DS samples [14]. Work presented in a previous study investigated SLM of the high temperature Ni-superalloy CM247LC [15]. It was found that CM247LC showed high susceptibility to cracking due to the high γ'

Fabrication of Blisk
To fabricate Fe-tooling SLM/HIP of CM247LC blisks, there are six detailed steps: a. The fabrication of blade tooling using an SLM process with Fe powder, Figure 1. To speed up building rates, processing conditions with a fast scan speed were selected (3000 mm/s at 300 W laser power). These conditions also had the benefit that the production of large amounts of black soot during processing was much reduced. b.
The components were sprayed with a thin layer of oil (WD40) before cutting from the substrate using Electrical Discharge Machining (EDM) to prevent rusting. c.
To avoid contaminating the powder, all of the parts, lid, base and SLM-processed tooling, were degreased with acetone in an ultrasonic bath before assembling, Figure 2. d. The assembled parts were welded together with a filling tube, Figure 3.

e.
After vacuum testing, the assembled parts were filled with CM247LC powder with a size range of 0-150 µm. The container was filled on a vibrating table to ensure good filling of the cavities and high, reproducible packing density. The filled can was degassed overnight and then sealed by crimping and welding. The sealed can was then HIPped at 1260 • C for 2 h. f.
The HIPped component was scanned with a Faro laser scanner. g.
The outer Fe-tooling was removed by pickling in nitric acid starting with concentrated acid (50%) for a day, diluted acid for 2-3 days and more dilute acid for 2 more days.
Micromachines 2020, 11, x FOR PEER REVIEW 3 of 17 e. After vacuum testing, the assembled parts were filled with CM247LC powder with a size range of 0-150 µm. The container was filled on a vibrating table to ensure good filling of the cavities and high, reproducible packing density. The filled can was degassed overnight and then sealed by crimping and welding. The sealed can was then HIPped at 1260 C for 2 h. f. The HIPped component was scanned with a Faro laser scanner. g. The outer Fe-tooling was removed by pickling in nitric acid starting with concentrated acid (50%) for a day, diluted acid for 2-3 days and more dilute acid for 2 more days.

Fe-tooling SLM/HIP of CM247LC Blisk with IN718 Inserted Disk
An additional study was carried out on a novel idea that uses a solid IN718 disk in the central blisk sections replacing much of the CM247LC powder, as shown in Figure 4a. The IN718 disk was cut from an ingot using EDM, and the recast layer was removed by pickling prior to assembly. The

Fe-tooling SLM/HIP of CM247LC Blisk with IN718 Inserted Disk
An additional study was carried out on a novel idea that uses a solid IN718 disk in the central blisk sections replacing much of the CM247LC powder, as shown in Figure 4a. The IN718 disk was cut from an ingot using EDM, and the recast layer was removed by pickling prior to assembly. The

Fe-tooling SLM/HIP of CM247LC Blisk with IN718 Inserted Disk
An additional study was carried out on a novel idea that uses a solid IN718 disk in the central blisk sections replacing much of the CM247LC powder, as shown in Figure 4a. The IN718 disk was cut from an ingot using EDM, and the recast layer was removed by pickling prior to assembly. The  from an ingot using EDM, and the recast layer was removed by pickling prior to assembly. The top lid was also further modified to improve degassing by adding extra grooves to locate the disc inside the can using a 1 mm deep step in the centre of the lid, seen in Figure 4b.
Micromachines 2020, 11, x FOR PEER REVIEW 4 of 17 top lid was also further modified to improve degassing by adding extra grooves to locate the disc inside the can using a 1 mm deep step in the centre of the lid, seen in Figure 4b.

Surface Finish
The surface finish of the blades was assessed using a profilometer (Ambios, XP-200, Ashprington, UK). As each cavity of the blade is inclined at 45 without any support structures during SLM processing, the sides of the blades have different surface finishes after SLM processing and HIPping. The measurement of surface roughness was carried out on both sides with 3 mm measuring distance. The roughness reported was the average of 3 measurements.

Microstructural Observation
For Fe-tooling SLM/HIP of CM247LC, a study of Fe diffusion was carried out to assess the processing parameters and to determine the allowance that will be required for machining. Samples were cut both from the HIPped can prior to and after the pickling followed by grinding and polishing for microstructural observation. The microstructural observation was carried out using a Jeol7000 Scanning Electron Microscope (SEM), fitted with backscattered and Energy Dispersive X-ray Spectroscopy (EDS) detectors. One of the blades was also cut from the component to observe the microstructures and assess consolidation after HIPping, especially at the thinnest part of the blade.

Mechanical Testing
For Fe-tooling SLM/HIP of CM247LC, both Room Temperature (RT) and Elevated Temperature (ET) tensile tests at 760 °C ± 3°C were performed (Westmoreland Mechanical Testing & Research, Limited) to assess the influence of the HIP processing parameters determined in this study. For the ET tests, the heating up time was approximately 60 mins and 30 mins for soaking time. Rod bars (measuring  = 8 mm, length = 55 mm) were cut from the HIPped and pickled blisk followed by machining according to ASTM E8-15a and ASTM E21-09 [27]. The bond line (between the powder and the solid part) was centred in the gauge length of the sample. All specimens were tested in strain rate controlled at 0.005 strain/min beyond yield at which point 0.05 strain/min was adopted and the extensometer was removed.

Results and Discussion
As for SLM/HIP of CM247LC, the work was performed using SLM to create a mild steel tooling (negative mould) of a blisk, Figure 5, whereby the sacrificial mild steel tooling, involved in the

Surface Finish
The surface finish of the blades was assessed using a profilometer (Ambios, XP-200, Ashprington, UK). As each cavity of the blade is inclined at 45 • without any support structures during SLM processing, the sides of the blades have different surface finishes after SLM processing and HIPping. The measurement of surface roughness was carried out on both sides with 3 mm measuring distance. The roughness reported was the average of 3 measurements.

Microstructural Observation
For Fe-tooling SLM/HIP of CM247LC, a study of Fe diffusion was carried out to assess the processing parameters and to determine the allowance that will be required for machining. Samples were cut both from the HIPped can prior to and after the pickling followed by grinding and polishing for microstructural observation. The microstructural observation was carried out using a Jeol7000 Scanning Electron Microscope (SEM), fitted with backscattered and Energy Dispersive X-ray Spectroscopy (EDS) detectors. One of the blades was also cut from the component to observe the microstructures and assess consolidation after HIPping, especially at the thinnest part of the blade.

Mechanical Testing
For Fe-tooling SLM/HIP of CM247LC, both Room Temperature (RT) and Elevated Temperature (ET) tensile tests at 760 • C ± 3 • C were performed (Westmoreland Mechanical Testing & Research, Limited) to assess the influence of the HIP processing parameters determined in this study. For the ET tests, the heating up time was approximately 60 mins and 30 mins for soaking time. Rod bars (measuring ∅ = 8 mm, length = 55 mm) were cut from the HIPped and pickled blisk followed by machining according to ASTM E8-15a and ASTM E21-09 [27]. The bond line (between the powder and the solid part) was centred in the gauge length of the sample. All specimens were tested in strain rate controlled at 0.005 strain/min beyond yield at which point 0.05 strain/min was adopted and the extensometer was removed.

Results and Discussion
As for SLM/HIP of CM247LC, the work was performed using SLM to create a mild steel tooling (negative mould) of a blisk, Figure 5, whereby the sacrificial mild steel tooling, involved in the production of a CM247LC SLM/HIP blisk, consists of a simple 'over-can' made by machining and the complex geometry SLM-processed blade tooling. The final version of the can and the blade tooling are shown in Figures 6 and 7. It is important that the can is filled completely, including the narrow blade sections shown in Figure 5. The final blade tooling was designed to have an extension, similar to a riser in casting, to ensure that each blade cavity is completely filled with powders.
Micromachines 2020, 11, x FOR PEER REVIEW 5 of 17 production of a CM247LC SLM/HIP blisk, consists of a simple 'over-can' made by machining and the complex geometry SLM-processed blade tooling. The final version of the can and the blade tooling are shown in Figure 6 and 7. It is important that the can is filled completely, including the narrow blade sections shown in Figure 5. The final blade tooling was designed to have an extension, similar to a riser in casting, to ensure that each blade cavity is completely filled with powders. The 'riser' was located at the thinnest part of the blade, with one for each blade, to ensure each cavity was filled with powder evenly; an extra groove ring was added to connect the 'risers' to provide a small powder reservoir to feed the cavities if required, as seen in Figure 7. The final assembled can design is shown in Figure 8. The filling tube was added at the welding stage.    production of a CM247LC SLM/HIP blisk, consists of a simple 'over-can' made by machining and the complex geometry SLM-processed blade tooling. The final version of the can and the blade tooling are shown in Figure 6 and 7. It is important that the can is filled completely, including the narrow blade sections shown in Figure 5. The final blade tooling was designed to have an extension, similar to a riser in casting, to ensure that each blade cavity is completely filled with powders. The 'riser' was located at the thinnest part of the blade, with one for each blade, to ensure each cavity was filled with powder evenly; an extra groove ring was added to connect the 'risers' to provide a small powder reservoir to feed the cavities if required, as seen in Figure 7. The final assembled can design is shown in Figure 8. The filling tube was added at the welding stage.    production of a CM247LC SLM/HIP blisk, consists of a simple 'over-can' made by machining and the complex geometry SLM-processed blade tooling. The final version of the can and the blade tooling are shown in Figure 6 and 7. It is important that the can is filled completely, including the narrow blade sections shown in Figure 5. The final blade tooling was designed to have an extension, similar to a riser in casting, to ensure that each blade cavity is completely filled with powders. The 'riser' was located at the thinnest part of the blade, with one for each blade, to ensure each cavity was filled with powder evenly; an extra groove ring was added to connect the 'risers' to provide a small powder reservoir to feed the cavities if required, as seen in Figure 7. The final assembled can design is shown in Figure 8. The filling tube was added at the welding stage.    The 'riser' was located at the thinnest part of the blade, with one for each blade, to ensure each cavity was filled with powder evenly; an extra groove ring was added to connect the 'risers' to provide a small powder reservoir to feed the cavities if required, as seen in Figure 7. The final assembled can design is shown in Figure 8. The filling tube was added at the welding stage.

The 1st Blisk
The detailed steps for fabricating Fe-tooling SLM/HIP CM247LC blisks were presented in the Experimental Methods section. After HIPping, from both top and bottom, a very shallow dip was apparent in the middle part of the component, where the disk formed after HIPping; the side of the component also shrank slightly towards the centre evenly from each direction, as shown in Figure 9. The HIPped component was scanned with a Faro laser scanner, as seen in Figure 10. It showed a small concave area close to the edge due to poor filling inside the groove, but the rest of groove showed no concave area.
After pickling using nitric acid, the steel tooling was removed and the netshape blisk was produced using Fe-tooling SLM/HIP, as shown in Figure 11. The fine risers were all filled with powder and became solid CM247LC pins connecting the blades and groove ring. The top and bottom of the disk sections were near to flat. Therefore, the can, including each blade, was filled with powder successfully before HIPping and consolidated into the complete blisk without any defects.

The 1st Blisk
The detailed steps for fabricating Fe-tooling SLM/HIP CM247LC blisks were presented in the Experimental Methods section. After HIPping, from both top and bottom, a very shallow dip was apparent in the middle part of the component, where the disk formed after HIPping; the side of the component also shrank slightly towards the centre evenly from each direction, as shown in Figure 9. The HIPped component was scanned with a Faro laser scanner, as seen in Figure 10. It showed a small concave area close to the edge due to poor filling inside the groove, but the rest of groove showed no concave area.
After pickling using nitric acid, the steel tooling was removed and the netshape blisk was produced using Fe-tooling SLM/HIP, as shown in Figure 11. The fine risers were all filled with powder and became solid CM247LC pins connecting the blades and groove ring. The top and bottom of the disk sections were near to flat. Therefore, the can, including each blade, was filled with powder successfully before HIPping and consolidated into the complete blisk without any defects.

The 1st Blisk
The detailed steps for fabricating Fe-tooling SLM/HIP CM247LC blisks were presented in the Experimental Methods section. After HIPping, from both top and bottom, a very shallow dip was apparent in the middle part of the component, where the disk formed after HIPping; the side of the component also shrank slightly towards the centre evenly from each direction, as shown in Figure 9. The HIPped component was scanned with a Faro laser scanner, as seen in Figure 10. It showed a small concave area close to the edge due to poor filling inside the groove, but the rest of groove showed no concave area.
After pickling using nitric acid, the steel tooling was removed and the netshape blisk was produced using Fe-tooling SLM/HIP, as shown in Figure 11. The fine risers were all filled with powder and became solid CM247LC pins connecting the blades and groove ring. The top and bottom of the disk sections were near to flat. Therefore, the can, including each blade, was filled with powder successfully before HIPping and consolidated into the complete blisk without any defects.

The 2nd Oversized Blisk
One of the concerns associated with HIPping is the need to consider the degree of shrinkage associated with powder consolidation. To assess the shrinkage of the first Fe-tooling SLM/HIP blisk due to HIPping, sectioned profiles were exported from 3D scanning GOM inspection software and measured in Solidworks. To accommodate shrinkages and machining, the second oversized SLM-processed blade tooling was designed based on sizes listed in Table 3. The size of the second tooling design is also limited by: (i) avoiding the need for a support structure within the blades during SLM processing; (ii) the diameter of the simple mild steel 'over-can' (limited by the size of the HIP vessel). The degassing of the first blisk was slow and therefore extra grooves were added on the top of the second (oversized) blade tooling, as shown in Figure 12.

The 2nd Oversized Blisk
One of the concerns associated with HIPping is the need to consider the degree of shrinkage associated with powder consolidation. To assess the shrinkage of the first Fe-tooling SLM/HIP blisk due to HIPping, sectioned profiles were exported from 3D scanning GOM inspection software and measured in Solidworks. To accommodate shrinkages and machining, the second oversized SLM-processed blade tooling was designed based on sizes listed in Table 3. The size of the second tooling design is also limited by: (i) avoiding the need for a support structure within the blades during SLM processing; (ii) the diameter of the simple mild steel 'over-can' (limited by the size of the HIP vessel). The degassing of the first blisk was slow and therefore extra grooves were added on the top of the second (oversized) blade tooling, as shown in Figure 12.

The 2nd Oversized Blisk
One of the concerns associated with HIPping is the need to consider the degree of shrinkage associated with powder consolidation. To assess the shrinkage of the first Fe-tooling SLM/HIP blisk due to HIPping, sectioned profiles were exported from 3D scanning GOM inspection software and measured in Solidworks. To accommodate shrinkages and machining, the second oversized SLM-processed blade tooling was designed based on sizes listed in Table 3. The size of the second tooling design is also limited by: (i) avoiding the need for a support structure within the blades during SLM processing; (ii) the diameter of the simple mild steel 'over-can' (limited by the size of the HIP vessel). The degassing of the first blisk was slow and therefore extra grooves were added on the top of the second (oversized) blade tooling, as shown in Figure 12.  The second (oversized) blisk was successfully fabricated, as shown in Figure 13a. Although it was entirely produced from powder like the second blisk, the top and bottom of the disk were nearly completely flat. A further GOM optical 3D scan was carried out, as shown in Figure 13b. It can be clearly seen that the blades are thicker than the first blisk, shown in Figure 11.

Blisk with IN718 Inserted Disk
To assess the utility of this approach for making multi-material/alloy structures, Fe-tooling SLM/HIP of a CM247LC blisk with an IN718 inserted solid disk was also attempted, as shown in Figure 14. The extra grooves filled with powder on the top of the component were revealed, which were added to the top lid to improve degassing and locate the IN718 disk inside the can. The second (oversized) blisk was successfully fabricated, as shown in Figure 13a. Although it was entirely produced from powder like the second blisk, the top and bottom of the disk were nearly completely flat. A further GOM optical 3D scan was carried out, as shown in Figure 13b. It can be clearly seen that the blades are thicker than the first blisk, shown in Figure 11.  The second (oversized) blisk was successfully fabricated, as shown in Figure 13a. Although it was entirely produced from powder like the second blisk, the top and bottom of the disk were nearly completely flat. A further GOM optical 3D scan was carried out, as shown in Figure 13b. It can be clearly seen that the blades are thicker than the first blisk, shown in Figure 11.

Blisk with IN718 Inserted Disk
To assess the utility of this approach for making multi-material/alloy structures, Fe-tooling SLM/HIP of a CM247LC blisk with an IN718 inserted solid disk was also attempted, as shown in Figure 14. The extra grooves filled with powder on the top of the component were revealed, which were added to the top lid to improve degassing and locate the IN718 disk inside the can.

Blisk with IN718 Inserted Disk
To assess the utility of this approach for making multi-material/alloy structures, Fe-tooling SLM/HIP of a CM247LC blisk with an IN718 inserted solid disk was also attempted, as shown in Figure 14. The extra grooves filled with powder on the top of the component were revealed, which were added to the top lid to improve degassing and locate the IN718 disk inside the can.

Surface Finish
As each cavity of the blade is inclined by 45 without any support structures during SLM processing, as such the sides of the blades have different surface finishes. The measurement of surface roughness was carried out on both sides with 3 mm measuring distance. The roughness was averaged over 3 measurements. The rougher surface showed an average Ra of 14.5 m, whereas it was 6.5 m on the smoother surface.

Blisk
A study of Fe diffusion from the sacrificial mild steel tooling was carried out to assess the depth of Fe-diffusion in order to determine the allowance that will be required for machining. It was found that the diffusion distance of Fe (measured using Energy-dispersive X-ray spectroscopy EDX) was ~163 m before the removal of the steel can (by pickling), as shown in Figure 15. Following pickling, the Fe diffusion layer was ~150 m, as shown in Figure 16. One of the blades was also cut from the component to observe the microstructure and assess its consolidation after HIPping focussing on the thinnest part of the blade. A limited area that was not fully consolidated was also observed; however, this was less than 10 m away from the edge, as shown in Figure 17a, and would therefore be removed during finishing. Prior Powder-Particle Boundaries (PPBs) were also more visible close to the thin edge of the blade, seen in Figure 17a. This could be due to the slightly higher oxygen content left at the thinnest area during degassing, which may provide nucleation sites for oxy-carbides. Again, those observed near to the edge of material that would be removed in the final machining. Further away from the edge showed nearly 100% density with evenly distributed precipitates ( Figure  17b). The diffusion of Fe requires machining of around 150 m and could incorporate techniques to achieve the appropriate surface finish necessary for an aerodynamic component.

Surface Finish
As each cavity of the blade is inclined by 45 • without any support structures during SLM processing, as such the sides of the blades have different surface finishes. The measurement of surface roughness was carried out on both sides with 3 mm measuring distance. The roughness was averaged over 3 measurements. The rougher surface showed an average Ra of 14.5 µm, whereas it was 6.5 µm on the smoother surface.

Blisk
A study of Fe diffusion from the sacrificial mild steel tooling was carried out to assess the depth of Fe-diffusion in order to determine the allowance that will be required for machining. It was found that the diffusion distance of Fe (measured using Energy-dispersive X-ray spectroscopy EDX) was 163 µm before the removal of the steel can (by pickling), as shown in Figure 15. Following pickling, the Fe diffusion layer was~150 µm, as shown in Figure 16. One of the blades was also cut from the component to observe the microstructure and assess its consolidation after HIPping focussing on the thinnest part of the blade. A limited area that was not fully consolidated was also observed; however, this was less than 10 µm away from the edge, as shown in Figure 17a, and would therefore be removed during finishing. Prior Powder-Particle Boundaries (PPBs) were also more visible close to the thin edge of the blade, seen in Figure 17a. This could be due to the slightly higher oxygen content left at the thinnest area during degassing, which may provide nucleation sites for oxy-carbides. Again, those observed near to the edge of material that would be removed in the final machining. Further away from the edge showed nearly 100% density with evenly distributed precipitates (Figure 17b). The diffusion of Fe requires machining of around 150 µm and could incorporate techniques to achieve the appropriate surface finish necessary for an aerodynamic component.

Blisk with IN718 Inserted Disk
A metallographic examination of the boundary between the IN718 disk and the HIPped CM247LC was carried out. There were high densities of Hf-rich precipitates (brighter particles on Back-scattered Electrons BSE) on the boundary (indicated by X-ray mapping) in Figure 18. It also showed that the chemical compositions varied cross the boundary, where Al and Co gradually increased from IN718 (left in BSE image) to CM247LC (right in BSE image), in contrast to Cr, Nb, Mo and Fe on X-ray maps, which decreased as seen in Figure 18.

Blisk with IN718 Inserted Disk
A metallographic examination of the boundary between the IN718 disk and the HIPped CM247LC was carried out. There were high densities of Hf-rich precipitates (brighter particles on Back-scattered Electrons BSE) on the boundary (indicated by X-ray mapping) in Figure 18. It also showed that the chemical compositions varied cross the boundary, where Al and Co gradually increased from IN718 (left in BSE image) to CM247LC (right in BSE image), in contrast to Cr, Nb, Mo and Fe on X-ray maps, which decreased as seen in Figure 18.

Mechanical Testing
The Ultimate Tensile Strength UTS (MPa), 0.2% proof stress (MPa) and % strain to failure of Fe-tooling SLM/HIPped CM247LC at RT and ET are shown in Figure 19, Figure 20, Figure 21 respectively. Data from conventionally cast and heat treated CM247LC [28] and previous work on powder HIPping of CM247LC undertaken in AMPLab [29,30] as well as vertically SLM-processed CM247LC [1] are represented for comparison. The 0.2% proof stress of samples was marginally higher at ET than RT due to the ordered γ phase. On comparing the various processing routes investigated in this work, including the work undertaken previously [29,30] and in this paper, HIPped CM247LC showed higher UTS and 0.2% proof stress than conventionally cast and heat treated CM247LC at both RT and ET, and slightly poorer ductility due to the presence of PPBs [28]. Moreover, it had superior UTS and ductility to vertically SLM-processed CM247LC at RT. The previous powder HIPped CM247LC samples [29,30] were tested at 750 • , which is slightly lower than that used in this study, therefore displaying higher ductility than Fe-tooling SLM/HIPped CM247LC. Figure 18. BSE micrographs of the boundary between the IN718 disk and the HIPped CM247LC powder, with a higher magnification BSE micrograph in the insert. X-ray maps of various elements are shown below the low magnification BSE.

Mechanical Testing
The Ultimate Tensile Strength UTS (MPa), 0.2% proof stress (MPa) and % strain to failure of Fetooling SLM/HIPped CM247LC at RT and ET are shown in Figure 19-21 respectively. Data from conventionally cast and heat treated CM247LC [28] and previous work on powder HIPping of CM247LC undertaken in AMPLab [29,30] as well as vertically SLM-processed CM247LC [1] are represented for comparison. The 0.2% proof stress of samples was marginally higher at ET than RT due to the ordered γ′ phase. On comparing the various processing routes investigated in this work, including the work undertaken previously [29,30] and in this paper, HIPped CM247LC showed higher UTS and 0.2% proof stress than conventionally cast and heat treated CM247LC at both RT and ET, and slightly poorer ductility due to the presence of PPBs [28]. Moreover, it had superior UTS and ductility to vertically SLM-processed CM247LC at RT. The previous powder HIPped CM247LC samples [29,30] were tested at 750°, which is slightly lower than that used in this study, therefore displaying higher ductility than Fe-tooling SLM/HIPped CM247LC.   [1]. Properties for conventionally cast and heat treated CM247LC are represented by the dashed line [28] and previous results of HIPped CM247LC undertaken in AMPLab by the solid line [29,30]. Figure 19. Bar plot showing Ultimate Tensile Strength (UTS) of HIPped CM247LC at Room Temperature (RT) and Elevated Temperature (ET), as well as SLM-processed CM247LC at RT for comparison [1]. Properties for conventionally cast and heat treated CM247LC are represented by the dashed line [28] and previous results of HIPped CM247LC undertaken in AMPLab by the solid line [29,30].

Figure 20.
Bar plot showing 0.2% proof stress of HIPped CM247LC at RT and ET, as well as SLMprocessed CM247LC at RT for comparison [1]. Properties for conventionally cast and heat treated CM247LC are represented by the dashed line [28] and previous results of HIPped CM247LC undertaken in AMPLab by the solid line [29,30].

[29,30] [28]
Figure 20. Bar plot showing 0.2% proof stress of HIPped CM247LC at RT and ET, as well as SLM-processed CM247LC at RT for comparison [1]. Properties for conventionally cast and heat treated CM247LC are represented by the dashed line [28] and previous results of HIPped CM247LC undertaken in AMPLab by the solid line [29,30].
Micromachines 2020, 11, x FOR PEER REVIEW 15 of 17 Figure 21. Bar plot showing % strain to failure of HIPped CM247LC at RT and ET, as well as SLMprocessed CM247LC at RT for comparison [1]. Properties for conventionally cast and heat treated CM247LC are represented by the dashed line [28] and previous results of HIPped CM247LC undertaken in AMPLab by the solid line [29,30].

Conclusion
Fe-tooling SLM/HIP of CM247LC was developed, and a can design which combines simple, mild steel 'over-can' tooling by machining with a complex blade tooling produced in low carbon steel by SLM successfully fabricated an oversized blisk. The initial component produced is of high quality. The HIPping parameters have been optimised based on an as-HIPped microstructure, the diffusion  [1]. Properties for conventionally cast and heat treated CM247LC are represented by the dashed line [28] and previous results of HIPped CM247LC undertaken in AMPLab by the solid line [29,30].

Conclusions
Fe-tooling SLM/HIP of CM247LC was developed, and a can design which combines simple, mild steel 'over-can' tooling by machining with a complex blade tooling produced in low carbon steel by SLM successfully fabricated an oversized blisk. The initial component produced is of high quality. The HIPping parameters have been optimised based on an as-HIPped microstructure, the diffusion of Fe and mechanical properties. The Fe diffusion was less than 150 µm indicating the need for limited final machining. Compared with conventionally cast and heat treated CM247LC, HIPped samples show higher UTS and 0.2% proof stress at both RT and ET and slightly poorer ductility. The roughness of the blades' surfaces was measured as 14.5 µm on the rougher side of the blades and 6.5 µm on the other side of the blades. A novel idea, Fe-tooling SLM/HIP of CM247LC blisk with IN718 inserted disk, was trialled and a hybrid component successfully produced. This is a potential area for future research as it has significant cost saving potential, with more effort required to improve the design of the interface between the two materials.