Nickel-based alloy powder comprising y2o3 oxide

Abstract

The present invention relates to a nickel-based alloy powder composed of 0.2 to 5% Y2O3 oxide, the remainder of the powder having the following composition: 0.050 to 0.090% C; 14.25 to 15.75% Co; 14.00 to 15.25% Cr; 4.00 to 4.60% Al; 3.90% to 4.50% Mo; 3.00 to 3.70% Ti; 0.012 to 0.020% B; 0 to 0.50% Fe; 0 to 0.060% Zr; 0 to 0.150% Mn; 0 to 0.20% Si; 0 to 0.10% Cu; 0 to 25 ppm S; 0 to 0.5 ppm Bi; 0 to 5 ppm Ag; 0 to 5 ppm Pb; 0 to 60 ppm N2; and 0 to 200 ppm O; Ni forming the balance of the composition; given that the percentages and ppm values mentioned hereinbefore are given with respect to the total of the remainder of the powder. The invention also relates to an alloy that can be produced from this powder and a method for producing the alloy from this powder.

Description

Description Title: Nickel-based alloy powder comprising Y2O3 oxide Technical field

[0001] This disclosure relates to the field of nickel-based alloys for aeronautical parts, as well as the field of alloy powders and processes for producing such alloys by laser powder bed fusion. Previous technique

[0002] Several materials are currently commercially available for the production of alloys by laser beam melting (also known as LBM), for example Inconel 718. However, this material cannot withstand temperatures exceeding 650°C. Yet, the operating environment temperature of a turbine or chamber is much higher.

[0003] Another available material is Hastelloy X, which can withstand temperatures up to 950°C, but is very limited mechanically and can only be used for manufacturing lightly loaded parts.

[0004] Similarly, the material CoCr (cobalt-based alloy) has been commercially developed. This alloy is used particularly for injection systems and can withstand temperatures of approximately 1000°C. However, it also has limited mechanical properties and is not suitable for the requirements of turbine components (blades and distributors).

[0005] For several years now, materials meeting the mechanical, thermal, oxidation, and corrosion requirements of these parts have been commercially available, and others are under development. One example is TIN738. However, it exhibits macrocracking problems that preclude its use in the intended applications. TIN939 and ABD900 are also worth mentioning. These two materials have only recently entered the market (less than two years ago), and their properties still need to be demonstrated and further developed. Finally, NK15CADT LBM has been available for longer but suffers from microcracking, which makes its manufacturing difficult. Furthermore, it remains limited to a maximum temperature of 1050°C.

[0006] Therefore, there is currently no alloy solution that allows temperatures above 1050°C to be reached while exhibiting good creep properties and good manufacturability.

[0007] NASA is developing alloys similar to the proposed alloy but based on different materials: https: / / ntrs.nasa.gov / citations / 20200000360. Specifically, two compositions are being considered: Composition 1: 32% cobalt; 30% chromium; 1.5% rhenium; 0.003% boron; nickel making up the balance; Composition 2: 33% cobalt; 29% chromium; 1.5% rhenium; and other percentages disclosed of aluminium, titanium, niobium, molybdenum, tungsten, zirconium, carbon and boron; nickel making up the balance.

[0008] Furthermore, university studies are also examining these possibilities, such as the one on IN625 ODS LBM: https: / / doi.org / 10.1016 / j.msea.2022.143813. This alloy is based on Inconel 625 to which up to 1.0% by weight of Y2O3 particles have been added. Inconel 625 has the following composition: at least 58.0% nickel; 20.0 to 23.0% chromium; up to 5.0% iron; 8.0 to 10.0% molybdenum; 3.15 to 4.15% niobium (plus tantalum); up to 0.10% carbon; up to 0.50% manganese; up to 0.50% silica; and up to 0.015% phosphorus. up to 0.015% sulfide; up to 0.40% aluminium; up to 0.40% titanium and up to 1.0% cobalt. Brief description of the invention

[0009] This disclosure improves the situation.

[0010] A nickel-based alloy powder is proposed, composed of 0.2 to 5% Y2O3 oxide, the remainder of the powder having the following composition: 0.050 to 0.090% C; 14.25 to 15.75% Co; 14.00 to 15.25% Cr; 4.00 to 4.60% Al; 3.90 to 4.50% Mo; 3.00 to 3.70% Ti; 0.012 to 0.020% B; 0 to 0.50% Fe; 0 to 0.060% Zr; 0 to 0.150% Mn; 0 to 0.20% Si; 0 to 0.10% Cu; 0 to 25 ppm S; 0 to 0.5 ppm Bi; 0 to 5 ppm of Ag; 0 to 5 ppm of Pb; 0 to 60 ppm of N2; and 0 to 200 ppm of O; Ni making up the balance of the composition; given that the percentages and ppm mentioned above are given relative to the total of the rest of the powder.

[0011] Other optional and non-limiting features are presented below.

[0012] Alloy powder can be composed of two particle populations: Y2O3 oxide particles and metallic particles that make up the remainder of the powder. The Y2O3 oxide particles can have dimensions ranging from 50 to 500 nm.

[0013] The alloy powder particles may have a metallic core made up of the composition and a surface layer made up of Y2O3 oxide around the metallic core.

[0014] The alloy powder can have the following particle size profile: D10 from 10 to 25 pm; D50 from 25 to 40 pm; and D90 from 40 to 70 pm.

[0015] The particles of the alloy powder can have a substantially spherical shape.

[0016] A nickel-based alloy is also proposed comprising: 0.050 to 0.090% C; 14.25 to 15.75% Co; 14.00 to 15.25% Cr; 4.00 to 4.60% Al; 3.90 to 4.50% Mo; 3.00 to 3.70% Ti; 0.012 to 0.020% B; 0 to 0.50% Fe; 0 to 0.060% Zr; 0 to 0.150% Mn; 0 to 0.20% Si; 0 to 0.10% Cu; 50 to 1000 ppm Y; 0 to 25 ppm S; 0 to 0.5 ppm Bi; 0 to 5 ppm Ag; 0 to 5 ppm Pb; 0 to 100 ppm of N2; 0 to 1000 ppm of O; 0 to 500 ppm of Pt; and 0 to 500 ppm of V; Ni making up the balance of the rest of the composition; given that the percentages and ppm mentioned above are given in relation to the weight of the total composition; the quantity of each of the other elements, called traces, being limited to 50 ppm with a total limited to 500 ppm.

[0017] A process for producing the alloy described above from the powder described above is also proposed. The process includes: preparing the powder by atomization; and melting the powder by laser powder bed fusion.

[0018] Other optional and non-limiting characteristics of the process are presented below.

[0019] The process may also include, after melting, hot isostatic compaction.

[0020] The process may further include at least one of the following treatments producing the following employment state: grain growth; resuspension and reprecipitation; and income.

[0021] In which case, the process may further include a de-stressing before the first of the treatments producing the employment state or after the last of the treatments producing the employment state. Brief description of the drawings

[0022] Other features, details, and advantages will become apparent upon reading the detailed description below and analyzing the attached drawings, on which: Fig. 1

[0023] [Fig. 1] schematically illustrates an embodiment of the Ni-based alloy powder of the present invention; in this embodiment, the alloy powder comprises two populations of particles: metallic particles and oxide particles. Fig. 2

[0024] [Fig. 2] schematically illustrates another embodiment of the Ni-based alloy powder of the present invention; in this other embodiment, the alloy powder is composed of particles having a structure comprising a metallic core and a surface layer of oxide. Fig. 3

[0025] [Fig. 3] schematically illustrates the steps of a process for producing a Ni-based alloy from the alloy powder of the invention; this process includes an atomization step and a melting step. Fig. 4

[0026] [Fig. 4] schematically illustrates the meander strategy of laser powder bed fusion usable for the fusion step of the process of developing the invention. Fig. 5

[0027] [Fig. 5] schematically illustrates the band strategy of laser powder bed fusion usable for the fusion step of the process of developing the invention. Fig. 6

[0028] [Fig. 6] schematically illustrates the contour strategy of laser powder bed fusion usable for the fusion step of the process of developing the invention. Fig. 7

[0029] [Fig. 7] schematically illustrates the island strategy of laser powder bed fusion usable for the fusion step of the process of developing the invention. Fig. 8

[0030] [Fig. 8] schematically illustrates the other optional steps in the process of developing a Ni-based alloy from the alloy powder of the invention, allowing the performance of the alloy to be improved according to the desired application. Description of the implementation methods

[0031] The present invention proposes a nickel-based alloy powder enabling the easy production by laser powder bed fusion of an alloy having good tensile strength, fatigue, creep and resistance to oxidation and corrosion up to at least 1100°C.

[0032] This alloy powder is composed of 0.2 to 5% Y2O3 oxide, the remainder of the powder having the following composition: 0.050 to 0.090% of C; 14.25 to 15.75% of Co; 14.00 to 15.25% Cr; 4.00 to 4.60% Al; 3.90 to 4.50% of MB; 3.00 to 3.70% Ti; 0.012 to 0.020% of B; 0 to 0.50% of Fe; 0 to 0.060% of Zr; 0 to 0.150% of Mn; 0 to 0.20% of Si; 0 to 0.10% Cu; 0 to 25 ppm of S; 0 to 0.5 ppm of Bi; 0 to 5 ppm of Ag; 0 to 5 ppm of Pb; 0 to 60 ppm of N2; and 0 to 200 ppm of O; Nor by balancing the composition; given that the percentages and ppm mentioned above are given in relation to the total of the rest of the powder.

[0033] The oxide Y₂O₃ may be present in the powder as nanometric PO particles (see Figure 1). In this case, the remainder of the powder consists of PM metallic particles. Thus, the alloy powder comprises two mixed particle populations: PM metallic particles and PO oxide particles. This mixture can be obtained by simple mechanical mixing, particularly using batch-mixing procedures.

[0034] Preferably, PO oxide particles have dimensions ranging from 50 to 500 nm. This characterization can be measured, in particular, by dynamic light scattering (DLS); the size corresponding to the peak of the particle size distribution is recorded. Instruments that allow this measurement include the Zetasizer Pro, Zetasizer Ultra, and Zetasizer Lab from Malvern Panalytical.

[0035] Preferably, the assembly of PM metallic particles has the following particle size profile: D10 from 10 to 25 pm; D50 from 25 to 40 pm; and D90 from 40 to 70 pm.

[0036] This particle size profile ensures the good processability of the alloy powder by laser powder bed fusion. Indeed, it allows for good powder bed compaction, good flowability, and also a reduction in melting stresses, which limits microcracking of the alloy.

[0037] PM metallic particles can be obtained by atomization, which ensures good morphology of the powder produced, particularly for particle sphericity. Atomization also helps to limit the risk of pollution.

[0038] Atomization can be carried out, for example, on René 77 powder, the chemical composition of which is as follows: 0.05 to 0.09% of C; 14.25 to 15.75% of Co; 14.00 to 15.25% Cr; 4.00 to 4.60% Al; 3.90 to 4.50% of MB; 3.00 to 3.70% Ti; 0.012 to 0.020% of B; 0 to 0.5% of Fe; 0 to 0.06% of Zr; 0 to 0.15% of Mn; 0 to 0.20% of Si; 0 to 0.10% Cu; 0 to 25 ppm of S; 0 to 0.5 ppm of Bi; 0 to 5 ppm of Ag; 0 to 5 ppm of Pb; 0 to 100 ppm of N2; 0 to 300 ppm of O; 0 to 500 ppm of Pt; and 0 to 500 ppm of V; the quantity of each of the other elements, called traces, being limited to 50 ppm with a total limited to 500 ppm.

[0039] Compared to René 77 powder, that of the present invention has a reduced S content of 25 ppm to ensure better resistance to oxidation and corrosion as well as a reduction in the risk of microcracking, while ensuring technical feasibility for atomization.

[0040] Sieving can be carried out after atomization to ensure that the particle size profile mentioned above is obtained.

[0041] The choice of starting powder, atomization and the sieving which is planned guarantees good control of the desired particle size and chemical composition, that is to say it allows to control well and reproducibly the size of the grains of powder obtained (particle size) and the chemical composition of the powder.

[0042] Alternatively, the particles in this powder typically have a metallic core (CM) made up of the composition and a surface layer (CS) made up of Y2O3 oxide surrounding the metallic core (CM) (see Figure 2). This ultimately results in a more uniform oxide distribution in the final material.

[0043] Preferably, the CS surface layer of oxide has a thickness of 50 to 500 nm, and always preferably a thickness of one grain of powder on the surface.

[0044] This powder particle structure can be obtained by mixing two populations of PM and PO particles, as described in the preceding paragraphs, notably by using a high-frequency oscillating mixer and applying stress. This process leads to the crushing of the PO oxide particles, which then form the surface oxide layers (CS), on the surface of the PM metallic particles, which form the CM metallic cores. The oscillating frequency can be 50 Hz or higher. The stress can be 50 MPa or higher.

[0045] In general, the powder can have the following particle size profile: D10 from 10 to 25 pm; D50 from 25 to 40 pm; and D90 from 40 to 70 pm.

[0046] This particle size profile ensures the good processability of the alloy powder by laser powder bed fusion. Indeed, it allows for good powder bed compaction, good flowability, and also a reduction in melting stresses, which limits microcracking of the alloy.

[0047] The particles of the alloy powder can have a substantially spherical shape.

[0048] Thus, this alloy powder, after laser melting on a powder bed, makes it possible to obtain a nickel-based alloy with the desired properties.

[0049] This alloy has the following chemical composition: 0.050 to 0.090% of C; 14.25 to 15.75% of Co; 14.00 to 15.25% Cr; 4.00 to 4.60% Al; 3.90 to 4.50% of MB; 3.00 to 3.70% Ti; 0.012 to 0.020% of B; 0 to 0.50% of Fe; 0 to 0.060% of Zr; 0 to 0.150% of Mn; 0 to 0.20% of Si; 0 to 0.10% Cu; 50 to 1000 ppm of Y; 0 to 25 ppm of S; 0 to 0.5 ppm of Bi; 0 to 5 ppm of Ag; 0 to 5 ppm of Pb; 0 to 100 ppm of N2; 0 to 1000 ppm of O; 0 to 500 ppm of Pt; 0 to 500 ppm of V; And Nor taking into account the balance of the rest of the composition; given that the percentages and ppm mentioned above are given in relation to the total weight of the composition; the quantity of each of the other elements, called traces, being limited to 50 ppm with a total limited to 500 ppm.

[0050] This alloy can notably be obtained from a manufacturing process using the alloy powder described above (figure 3).

[0051] This manufacturing process includes: the S01 preparation of the powder by atomization; SO2 fusion of powder by laser powder bed fusion.

[0052] Powder bed fusion (PBF) is an additive manufacturing technique used primarily for the production of metal parts. It involves spreading a thin layer of metal powder onto a platform, then using a high-power laser to selectively melt the powder particles along a path defined by a 3D digital model. The laser melts the metal powder along its path over a line width, leaving behind a line or bead of solidified metal. After the layer solidifies in the desired areas, a new layer of powder is deposited, and the process is repeated layer by layer until the complete part is formed. In this process, the unsolidified metal powder is not removed, as it serves as a substrate for the next layer. This process allows for to produce complex parts with high precision and excellent level of detail, while minimizing material waste.

[0053] SO2 fusion is carried out under a neutral atmosphere, preferably under an atmosphere of argon or nitrogen.

[0054] Laser SO2 powder bed fusion can be achieved using a laser power of 150 W to 300 W.

[0055] The laser's travel speed is from 900 mm / s to 1300 mm / s.

[0056] The thickness of the layers is preferably 20 to 60 µm.

[0057] The line width is preferably 50 to 200 µm. Alternatively, the overlap between fusion lines is 20 to 150 µm. The overlap between fusion lines refers to the width of the gap between the areas to which laser power is applied between two adjacent lines. This overlap prevents insufficient fusion of the alloy in an interstitial zone between two lines because the laser power is not constant across the entire laser spot and varies slightly towards the periphery.

[0058] There are several strategies for fusing the entire surface S required to manufacture the desired part onto a single layer: meander, band, contour, and island. In the meander strategy (see Figure 4), the laser traces a back-and-forth path L (the direction of laser movement is indicated by the arrows in the figures) across the entire width of the surface S of the powder bed P to be fused. In the band strategy (see Figure 5), the surface S of the powder bed P to be fused is divided into bands B, and the laser traces a back-and-forth path L between the lateral boundaries of one band B before moving to another band B (in Figure 5, the back-and-forth path is shown in only one band for clarity). In the contour strategy (see Figure 6), the laser first traces the contour of the surface S of the powder bed P to be fused, and then its path follows this contour while progressing inward toward the center of the surface S to be fused.Finally, in the island strategy (see figure 7), the surface S of the powder bed P to be fused is divided into small zones Z in each of which the laser describes a back-and-forth L (in figure 7, the back-and-forth path is only shown on four adjacent zones for readability reasons); the orientation of the back-and-forth L can change from one zone Z to another, for example undergoes a 90° rotation from one zone to another adjacent one.

[0059] Here, although all strategies are usable, the banding strategy is preferred. In this case, the band width can be from 2 to 15 mm. The overlap between bands can be from 0.05 to 0.15 mm. Band overlap refers to the width of the overlap between the areas to which laser power is applied between two adjacent bands. This overlap prevents insufficient fusion of the alloy in an interstitial zone between two adjacent bands because the laser power is not constant across the entire laser spot and varies slightly towards the periphery.

[0060] The orientation of the B bands may be different from one layer to another, preferably it undergoes a rotation of 60 to 75°, preferably 65 to 70°, for example 67° between two successive layers.

[0061] These fusion parameters ensure sufficient energy input during fusion, while limiting residual stresses and microcracking.

[0062] During this SO2 melting process, the oxide, which is very small, dissolves uniformly within the material matrix and serves as anchoring zones for the dendrites during solidification, thus preventing the formation of interdendritic microcracks. In some cases, a few oxide particles may remain in the alloy matrix. However, these rare residual oxide particles do not compromise the alloy's performance.

[0063] The alloy composition given above is obtained after this SO2 melting process. The only elements modified compared to the initial metal particles are the O, Y, and N2 content, as well as the addition of trace elements. The modification of the O and N2 content is associated with i) the absorption of these elements during the melting of the powder grains, ii) the absorption of these elements within the manufacturing chamber from the unmelted powder, which is then reused for subsequent production runs (recycling), and iii) the addition of the Y2O3 oxide. The modification of the Y content results directly from the added oxide. Industrially, it is therefore necessary to plan for an increase in the concentration between the powder and the fused material. These concentrations are fixed with regard to the mechanical properties obtained and industrial capabilities.

[0064] Several treatments can then be carried out after melting to improve the alloy's properties depending on the intended application (see Figure 8). These treatments include: hot isostatic compaction S03; a growth of grains S05; a return to solution S06 and reprecipitation S06'; and an S07 income.

[0065] Grain growth S05, resuspension S06 and reprecipitation S06', and income S07 are said to be treatments producing the employment state.

[0066] Only one of these treatments may be prescribed, or a combination of at least two of them. In the case of a combination, the treatments are carried out in this order, eliminating any unnecessary treatments.

[0067] Hot isostatic pressing (HIP) S03 increases the alloy's density. HIP S03 involves applying high temperature and pressure to complete the melting process, filling in areas where melting was insufficient in the alloy.

[0068] Hot isostatic compaction S03 can be carried out at a temperature of 1190 to 1210 °C, preferably 1195 to 1205 °C, for example 1200 °C. The applied pressure is preferably above 100 MPa. The maintenance time at this temperature and pressure is at least 4 hours and may exceed this duration by 20%.

[0069] Grain growth in SO5 allows for an increase in the size of the metallurgical grain. Indeed, the grain size is relatively small as it comes out of the melt, on the order of 2 to 7 ASTM. However, creep properties are better when the grain size is larger, as in foundry work with a grain size of around 00 ASTM (in the ASTM notation, the higher the number, the smaller the grain size). This treatment aims to achieve a grain size of 00 to 5 ASTM, which guarantees good creep, tensile, and fatigue properties; therefore, it is suitable for turbine blades and distributors. It is particularly advantageous for manufacturing parts intended to be subjected to creep stresses, such as distributors and turbine blades.In other cases it is not necessary, for example chamber parts, turbine sealing sectors or OSAS, retaining rings or cladding parts which are not subject to creep stresses.

[0070] Grain growth in S05 is typically achieved through high-temperature quenching, particularly after hot isostatic pressing (S03). Quenching can be carried out at a temperature of 1220 to 1240 °C, preferably 1225 to 1235 °C, for example, 1230 °C. The holding time at this temperature can be 5 hours and may exceed this value by 20%. Upon completion of this treatment, the alloy is simply exposed to air.

[0071] Resolution (S06) dissolves secondary phase particles or precipitates within the alloy matrix, resulting in improved compositional homogeneity. Resolution is followed by reprecipitation (S06').

[0072] Typically, the SO6 resolution can be achieved by heating the alloy to a temperature of 1150 to 1170 °C, preferably 1155 to 1165 °C, for example 1160 °C. The holding time at this temperature is advantageously 2 hours and can exceed this value by 20%.

[0073] The S06' reprecipitation is obtained by controlling the cooling. This cooling can be carried out in the oven up to 1080 °C at a rate of 47 to 67 °C / h, preferably 52 to 62 °C / h, for example 57 °C / h; then from 1080 °C to 540 °C at a rate greater than or equal to 16 °C / min to finish in air after 540 °C.

[0074] Tempering S07 provides a slight improvement in tensile properties. When this improvement is not desired, it is unnecessary. It can be achieved by heating the alloy to a temperature of 750 to 770 °C, preferably 755 to 765 °C, for example, 760 °C. The holding time for this heating is typically 4 hours and can exceed this value by 20%. After this treatment is complete, the alloy is simply exposed to air.

[0075] A stress-relieving treatment S04, which removes any remaining stresses within the alloy matrix, can be carried out before the first treatment applied among the treatments producing the service condition.

[0076] This S04 release is typically carried out under the same conditions described above for the S07 revenue.

[0077] This S08 detention can alternatively or additionally be carried out after the S07 return.

[0078] These treatments allow for an HV hardness of 350 to 475 HV and properties at the expected levels (notably: no impact on physical properties such as density, Poisson's ratio, Young's modulus, thermal expansion, electrical / thermal conductivity, and specific heat; and on cracking properties; as well as an increase in tensile, creep, and fatigue properties), making them particularly suitable for targeted parts where microcracking is eliminated or at least significantly reduced. A slight anisotropy may be observed. This is typical of laser powder bed fusion and is not problematic for the alloy's properties. The addition of the oxide allows for a gain of around 30% in tension, creep and fatigue at 1100°C and does not result in a drop in the properties of the alloy up to 1150°C (compared to 1050°C for the best alloys available today such as René 77 without oxide).

[0079] The present invention also provides an aeronautical part manufactured from the alloy described above. This part is formed directly during the melting process described above. The aeronautical part may be, in particular, a turbine distributor, a retaining ring, a sealed sector (OSAS), an injection system, a fairing component, or a turbine blade.

Claims

Demands

1. Nickel-based alloy powder composed of 0.2 to 5% Y2O3 oxide, the remainder of the powder having the following composition: 0.050 to 0.090% of C; 14.25 to 15.75% of Co; 14.00 to 15.25% Cr; 4.00 to 4.60% Al; 3.90 to 4.50% of MB; 3.00 to 3.70% Ti; 0.012 to 0.020% of B; 0 to 0.50% of Fe; 0 to 0.060% of Zr; 0 to 0.150% of Mn; 0 to 0.20% of Si; 0 to 0.10% Cu; 0 to 25 ppm of S; 0 to 0.5 ppm of Bi; 0 to 5 ppm of Ag; 0 to 5 ppm of Pb; 0 to 60 ppm of N2; and 0 to 200 ppm of O; Nor by balancing the composition; given that the percentages and ppm mentioned above are given in relation to the total of the rest of the powder.

2. Alloy powder according to claim 1, composed of two populations of particles: Y2O3 oxide particles (PO) and metallic particles (PM) constituting the remainder of the powder.

3. Alloy powder according to claim 1, wherein the Y2O3 (PO) oxide particles have dimensions ranging from 50 to 500 nm.

4. Alloy powder according to claim 1, wherein the particles have a metallic core (CM) made up of the composition and a surface layer (CS) made up of Y2O3 oxide around the metallic core.

5. Alloy powder according to any one of claims 4, having the following particle size profile: D10 from 10 to 25 pm; D50 from 25 to 40 pm; and D90 from 40 to 70 pm.

6. Alloy powder according to any one of claims 1 to 5, wherein the alloy powder particles have a substantially spherical shape.

7. Nickel-based alloy comprising: 0.050 to 0.090% of C; 14.25 to 15.75% of Co; 14.00 to 15.25% Cr; 4.00 to 4.60% Al; 3.90 to 4.50% of MB; 3.00 to 3.70% Ti; 0.012 to 0.020% of B; 0 to 0.50% of Fe; 0 to 0.060% of Zr; 0 to 0.150% of Mn; 0 to 0.20% of Si; 0 to 0.10% Cu; 50 to 1000 ppm of Y; 0 to 25 ppm of S; 0 to 0.5 ppm of Bi; 0 to 5 ppm of Ag; 0 to 5 ppm of Pb; 0 to 100 ppm of N2; 0 to 1000 ppm of O; 0 to 500 ppm of Pt; and 0 to 500 ppm of V; Nor balancing the rest of the composition; given that the percentages and ppm mentioned above are given in relation to the weight of the total composition; the quantity of each of the other elements, called traces, being limited to 50 ppm with a total limited to 500 ppm.

8. A process for producing the alloy according to claim 7 from the powder according to any one of claims 1 to 6, the process comprising: the preparation (S01) of the powder by atomization; the fusion (SO2) of the powder by laser powder bed fusion.

9. Method according to claim 8, further comprising after melting, hot isostatic compaction (SO3).

10. A process according to claim 8 or claim 9, further comprising at least one of the treatments producing the following use state: grain growth (S05); a resolution (S06) and reprecipitation (S06'); and an income (S07).

11. A process according to claim 10, comprising a detensioning (S04, S08) before the first of the treatments producing the use state or after the last of the treatments producing the use state.

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