Aluminum powder material for manufacturing products using additive manufacturing methods

Abstract

The present invention relates to the field of powder metallurgy, particularly to a powder material primarily composed of an aluminum alloy, which is used for additive manufacturing, particularly selective laser melting, to produce additively manufactured articles. The aluminum powder material contains 33.00-45.00 mass% silicon, 1.00-3.00 mass% nickel, 0.10-1.00 mass% zirconium, 0.10-0.80 mass% chromium, 0.05-0.50 mass% titanium, 0.10-0.80 mass% iron, 0.005-0.10 mass% strontium and / or phosphorus, 0.02 mass% or less copper, 0.02 mass% or less manganese, and 0.02 mass% or less magnesium. The aluminum powder material is used for additively manufacturing products that will be used in contact with stainless steel. To produce the additively manufactured articles, 17.10 -6 °С -1 A low thermal expansion coefficient of 200 MPa or less and a yield strength of 200 MPa or more are ensured.

Description

[Technical Field]

[0001] The present invention relates to the field of metallurgy, in particular to powder materials based on aluminum alloys, which are used to manufacture products using additive manufacturing methods. [Background technology]

[0002] Additive manufacturing is a technique for building three-dimensional objects by layer-by-layer deposition (addition) of powdered materials such as plastic, metal, or concrete. Depending on the end result, additive manufacturing can be used in several ways to manufacture products such as parts, molds, and finished products. There are various additive manufacturing methods and materials used, some of which are based on melting or softening the material, such as selective laser sintering, selective laser melting, direct metal laser sintering, and fused deposition modeling.

[0003] The tendency of metallic materials and products to spontaneously change shape and dimensions during manufacturing or use, including at high temperatures, is a factor that hinders the accurate operation of mechanical devices. Changes in geometric dimensions of parts and products during manufacturing and use are primarily due to the structural instability of materials, i.e., the existence of phase transformations within the temperature range in which the products are used, and the relaxation of residual internal stresses induced in parts during manufacturing.

[0004] The primary alloying element used to produce aluminum alloys with a given CTE (coefficient of thermal expansion) is silicon (Si has a CTE of 5.1·10 -6 K -1 In this context, hypereutectic Al-Si alloys (with silicon content of 12% or more) are most commonly used to manufacture parts that require high thermal stability and dimensional stability over temperature. These alloys have a low CTE close to that of steel, high wear resistance, strength and hardness in high-temperature environments, good corrosion resistance, and a high strength-density correlation.

[0005] Since the 1970s, CTE <20·10 ensures geometric dimensional stability of the product even when the ambient temperature changes.-6 K -1 A series of alloys with low thermal expansion coefficients have been developed. These alloys have also become widely used in precision engineering when building small or rigid structures. The best-known aluminum sintered alloys in this field, ASA-1 and ASA-2, have low linear expansion coefficients (14-16·10 -6 K -1 These alloys are used in equipment parts that operate at room temperature, where a combination of low specific gravity and high mechanical strength is required. These alloys are the most popular silumins, such as AlSi10Mg (CTE 21·10 -6 K -1 ), it has a significantly lower CTE at test temperatures between 20 and 200 °C. The main disadvantages of this series of alloys are the high price of the products, which is caused by the expensive manufacturing process, which is characterized by the high cost of manufacturing press tools, the low material utilization factor during machining, and the inability to obtain products with complex geometric shapes.

[0006] Additive manufacturing techniques allow for the production of complex shapes with a high material utilization factor and minimal machining to a specified degree of precision.

[0007] The most widely known aluminum material used in additive manufacturing techniques is the Al-Si alloy AlSi10Mg, which contains 9-11% silicon and 0.20-0.60% magnesium by mass. AlSi10Mg alloy has a tensile strength of 320 MPa, a yield strength of 210 MPa, and a CTE of 21·10. -6 K -1 It has excellent manufacturability in selective laser melting, but its low thermal stability and high CTE value have prevented it from being fully put to practical use in precision equipment manufacturing.

[0008] In this context, there is currently a challenge to develop materials with defined mechanical properties and coefficient of thermal expansion (CTE) within the operating temperature range for additive manufacturing.

[0009] A method for manufacturing a metal part using an aluminum alloy is known (WO2017077137A9 published on July 6, 2017). In addition to the main alloying elements, the content of impurities intentionally added to achieve specific functional properties of the alloy, or unintentional impurities contained in the main alloying elements or waste used to manufacture the alloy, is regulated. The maximum content of each of the following impurity elements is 1.8% or less, but for some elements, 0.03% or less is desirable.

[0010] The main drawback of this alloy is its high copper (up to 20%) and magnesium (up to 50%) contents, which increase the crystallization interval of the alloy and cause hot cracking in the alloy structure. Also, the general over-alloying of the alloy can cause cold cracking during selective laser melting due to high internal stresses caused by the release of numerous intermetallic compounds. Furthermore, the introduction of scandium (up to 10% by mass) into the alloy composition significantly increases the manufacturing costs of products made from this alloy.

[0011] The prior art is known for composite powder materials containing silicon, nickel, beryllium, aluminum oxide, and carbon, which are produced by mechanical alloying and subsequent consolidation by vacuum forming (Patent RU 2353689 published on April 27, 2009 and Patent RU 2394928 published on July 20, 2010). The resulting materials have a homogeneous dispersion structure and offer high stability of precision elastic properties.

[0012] The main drawback of the proposed composite is the complexity of its manufacturing process, which involves a vacuum compaction process, resulting in the inability to obtain complex shaped products with internal channels or cellular structures. Another drawback is the use of beryllium, a toxic element, in its composition.

[0013] The prior art is known from patent RU 2468105, published on 27 November 2012, of a deformable aluminum alloy for the manufacture of pistons, the composition of which is mainly aluminum and further comprises the following components: Silicon 16.0 to 19.5 mass% Copper 3.0~5.0% by mass Magnesium 0.7 to 1.2 mass% Manganese 0.3 to 0.7 mass% Iron 0.9 to 1.5 mass% Titanium 0.2 to 0.5 mass% Zirconium 0.15 to 0.4 mass% Aluminum oxide 0.01 to 0.3 mass% Cerium 0.001~0.005% by mass Nickel 1.3% by mass or less

[0014] The composition of the proposed alloy ensures wear resistance and high strength at room and elevated temperatures. The main drawback of the proposed alloy is its low tensile strength. -6 K -1 This is due to the relatively low content of silicon and the presence of copper, magnesium, and manganese in the composition, which all have high CTEs. Furthermore, the high content of copper and magnesium in the composition can adversely affect the manufacturability of the alloy when used in selective laser melting, due to the occurrence of hot cracking in the structure of the molten material.

[0015] As prior art, a composite powder material (patent RU 2639088 published on December 19, 2017) is known, the composition of which contains the following components: Copper 4~6% by mass Boron carbide 1-8% by mass Aluminum Remaining

[0016] The main drawback of a given composite material is 19-21·10 depending on the alloying element content. -6 K -1 The CTE level of the material is insufficient to achieve this. Additionally, the high copper content in the composition can lead to hot cracking during selective laser melting.

[0017] The prior art is known from a composite powder material (patent RU 2533512 published on 20 November 2014) which has become a prototype material, the composition of which contains the following components: Silicon 41-45.4% by mass Nickel 3.9 to 5.6 mass% Aluminum oxide ≦2.8 mass% Iron ≦0.48% by mass Aluminum Remaining

[0018] The resulting material has high dimensional stability, low specific gravity, and a CTE of 12·10 -6 K -1 The main drawback of the above composite powder materials is the complexity of their manufacturing process, which involves mechanical alloying of the mixture and gas isostatic pressing in an aluminum capsule, and as a result, it is not possible to obtain products with complex shapes without subjecting the resulting blanks to additional mechanical processing.

[0019] The uniformity of the CTE of the mixed materials is important in terms of maintaining the dimensional stability of the product, alignment of components, compliance with technical gaps, tightness of joints, wave properties, etc. The CTE of most stainless steels used in equipment engineering (austenitic stainless steels in the 300 series, such as AISI 316L, AISI 304, AISI 309) is 15-17·10 -6 K -1 Therefore, to replace some or all of the components of a product, a CTE of 17·10 -6 K -1It is necessary to use aluminum alloys with a CTE of 30% or less (alloys with a silicon content of 30% or more). At the same time, by replacing stainless steel with aluminum alloys, the weight of the device can be reduced while maintaining its technical properties. For example, using an aluminum alloy with a low CTE instead of stainless steel for the manufacture of complex-shaped waveguides can reduce the mass of the device (waveguide + illuminator, made of stainless steel) while maintaining the loss characteristics and standing wave ratio within the waveguide. Using an aluminum alloy with a low CTE as the base for the reflective surfaces and frame structure of various optical devices can reduce the mass of the device while maintaining low values ​​of distortion due to thermal expansion when the optical device is heated. Summary of the Invention [Problem to be solved by the invention]

[0020] The technical problem and technical achievement of the present invention are to manufacture products that are used in contact with various stainless steels using additive manufacturing technology. -6 °С -1 The objective of this project is to develop and manufacture a new aluminum powder material with a low thermal expansion coefficient of 1000 MPa or less and a yield strength of 200 MPa or more. [Means for solving the problem]

[0021] To address this issue, a method for producing a consolidated aluminum powder material using additive manufacturing techniques was developed. This manufacturing method ensures dimensional stability and strength in products used in contact with stainless steels and other materials with similar temperature coefficients of linear expansion (TCLE) at various temperatures. This is made possible in particular by the formation of primary silicon crystals of less than 20 μm in size within the resulting material, which are uniformly distributed throughout the material, and by the improved matrix strength due to solid solution strengthening and dispersion strengthening by thermally stable phases.

[0022] This technical problem is solved and the technical result achieved by obtaining an aluminum powder material containing the elements in the following ratios: Silicon 33.00 to 45.00 mass% Nickel 1.00 to 3.00 mass% Zirconium 0.10 to 1.00 mass% Chromium 0.10 to 0.80 mass% Titanium 0.05 to 0.50 mass% Iron 0.10 to 0.80 mass% Strontium and / or phosphorus 0.005 to 0.10 mass% Copper 0.02% by mass or less Manganese 0.02% by mass or less Magnesium 0.02% by mass or less Aluminum and unavoidable impurities Remaining

[0023] The powder material preferably has a particle size distribution of 20 to 150 μm, and most preferably 20 to 63 μm. The powder material can be obtained by gas atomization in a nitrogen or argon atmosphere, or by gas atomization in a nitrogen or argon atmosphere with the addition of 0.1 to 0.8 mass% oxygen. The powder material has a particle size distribution of 17·10 -6 °С -1 It has a thermal expansion coefficient of 0.1% or less and a yield strength of 200 MPa or more.

[0024] Also claimed is a method of manufacturing an article using additive manufacturing techniques using the aluminum powder material described above.

[0025] Also claimed are products made from the above-described aluminum powder material. [Brief explanation of the drawings]

[0026] Shown in the drawings are the following: [Figure 1] 1 shows the appearance of particles of the alloy powder of the present invention obtained by gas atomization in Example 1. [Figure 2] 1 shows the cross-sectional structure of a powder particle. [Figure 3] Appearance of a cubic specimen fabricated to determine the optimal parameters for selective laser melting. [Figure 4] The structure of the material of the fifth alloy in Example 1. [Figure 5] Macrocracks in the structure of a prototype material obtained by selective laser melting technology. [Figure 6] Microstructure of the prototype material obtained by selective laser melting technique. [Figure 7] Appearance of the sample substrate according to GOST 1497-84 standard. [Figure 8] Structural appearance of test specimens of Alloy A described in Example 2, annealed at 350°C for different times. [Figure 9] 1. View of the platform carrying the products (concave / convex mirror blanks) manufactured from the material of the present invention using selective laser melting technology. DETAILED DESCRIPTION OF THE INVENTION

[0027] The silicon content of 33.00-45.00% by mass was chosen based on the need to ensure low values ​​of thermal expansion. This upper limit was chosen based on the fact that during crystallization during printing, primary silicon crystals are initially formed, which significantly increase the brittleness of the material, resulting in cracks in the printed product.

[0028] Alloying with 0.10-0.80 wt% iron promotes the formation of insoluble intermetallic inclusions based on aluminum, silicon, and iron, leading to further hardening of the matrix and improving the thermal stability of the alloy. Iron does not increase the cost of the alloy and does not adversely affect the increase in TCLE.

[0029] The addition of 1.00-3.00 wt.% nickel was selected to ensure the alloy's required coefficient of thermal expansion and manufacturability through the formation of the Al3Ni eutectic phase, which improves the alloy's liquid fluidity and reduces the likelihood of hot cracking during additive manufacturing. The Al3Ni phase also provides high thermal stability, allowing the material to maintain its properties during heat treatment and at high service temperatures. Nickel also mitigates the negative effect of iron on ductility through the formation of a co-existing ternary phase and the reduction of the aluminum-, iron-, and silicon-based phases.

[0030] Alloying with 0.10-1.00 wt% zirconium, 0.10-0.80 wt% chromium, and 0.05-0.50 wt% titanium promotes dispersion strengthening of the alloy matrix as a result of the breakdown of the solid solution during heat treatment. Chromium also inhibits the diffusion of nickel in solid solution during heat treatment, promoting the formation of small Ni3Al crystals uniformly distributed throughout the matrix, which increases the strength and thermal stability of the matrix. The zirconium, chromium, and titanium contents are limited because high contents of these elements significantly increase the number of intermetallic compounds, increasing internal stresses and the low ductility of Al-33-45%Si alloys, which can lead to cold cracking during selective laser melting.

[0031] The addition of 0.005 to 0.10% by weight of strontium and / or phosphorus promotes spheroidization and grinding of the particles of primary silicon, which has a positive effect on the strength properties of the material of the invention. In the alloy of the present invention, the contents of copper, manganese, and magnesium are limited to 0.02 wt.% or less because these elements have a high CTE and their introduction into the alloy adversely affects the overall CTE of the alloy. High contents of copper and magnesium increase the crystallization interval of the alloy, which can lead to hot cracking during rapid crystallization of the alloy. Magnesium also worsens the high-temperature brittleness of the alloy, adversely affecting its manufacturability during printing. In addition, the formation of manganese-based intermetallic compounds requires high-temperature treatment, which can cause the growth of primary silicon crystals and the growth of Al3Zr phases, adversely affecting the strength properties of the alloy.

[0032] The following techniques can be used to produce aluminum powder materials: Preparation of aluminum-based melts of the required chemical composition using pre-melted material or material melted directly in the crucible of the atomizer; The alloy melt is gas atomized using a vertical or horizontal atomizer (nitrogen, argon, or a mixture of these with oxygen can be used). The resulting spray is subjected to sieving and gas dynamic separation to separate the desired particle size from the powder.

[0033] The invention is illustrated by the following examples. [Example]

[0034] A melt of aluminum of grade A7 or higher conforming to GOST 11069-2001 was prepared in the furnace of a horizontal atomizer. Then, while maintaining the melt temperature, Si00-grade crystalline silicon conforming to GOST 2169-69 was introduced in several stages. After the silicon was completely melted, H0-grade metallic nickel conforming to GOST 849-2008, X99-grade metallic chromium conforming to GOST 5905-2004, and master alloys AlZr15 and AlTi5 conforming to GOST R 53777-2010 were introduced, followed by Fe80F20 tablets of iron (80% Fe, 20% flux).

[0035] After all the introduced master alloys had melted, the slag was removed and carnallite flux was added to the surface of the melt at a rate of 2 kg / t (to reduce the loss of alloying elements). After the flux had melted, AlSr5 and / or P grade master alloys conforming to GOST R 53777-2010 were introduced under the flux layer, and the slag was removed and samples taken to control the chemical composition.

[0036] The manganese, magnesium and copper contents were ensured by the purity of the master alloy used.

[0037] The powder was produced in a horizontal gas atomizer using a nitrogen and oxygen gas mixture containing less than 0.8% oxygen. The atomized spray was then sieved and gas-dynamically separated to separate particles of the target particle size range of 20-63 μm, with a D50 of 45±3 μm. Scanning electron microscope images of the powder granules and their cross sections are shown in Figures 1 and 2, respectively.

[0038] The chemical composition of the obtained powder (Table 1) was identified using an inductively coupled plasma atomic emission spectrometer, and the particle size distribution of the powder was investigated by laser diffraction.

[0039] [Table 1]

[0040] The manufacturability of the resulting powder materials during selective laser melting was investigated. An EOS M 290 selective laser melting machine was used for this purpose. For each material, cubic specimens (10x10x10) were fabricated using individual melting modes, including settings for laser power, scanning speed, and inter-track distance. The laser power was varied from 200 to 370 W, the scanning speed from 400 to 2000 mm / s, and the inter-track distance from 0.075 to 0.22 mm. Figure 3 shows the external view of the platform on which the fabricated cubic specimens were placed.

[0041] The presence or absence of defects in the fabricated metal structures was controlled by microsections cut along the fabrication direction (perpendicular to the layers). The number of porosity, unmelted areas, hot cracks, and cold cracks was measured in at least five different fields of view of the test cross section using bright-field light microscopy at 100x magnification. The percentage of porosity and unmelted areas was calculated as the arithmetic mean value obtained from the investigated fields. Figure 4 shows an example of the optimal structure (scanning electron microscope image) for the fifth material listed in Table 1. Selective laser melting of the prototype material (Table 1) resulted in the formation of macrocracks over a wide range of energy rate parameters. Figure 5 shows an image of macrocracks in the fabricated prototype material structure. Figure 6 shows the microstructure of the prototype material after selective laser melting. It can be seen that the cracks propagated through both the eutectic phase and the primary silicon crystals. This indicates that these cracks were cold cracks, caused by large internal residual stresses that developed after the molten pool solidified.

[0042] After determining the optimal parameters for selective laser melting, cylindrical specimens with a diameter of 14 mm and a length of 85 mm were fabricated in two orientations, parallel and perpendicular to the growth direction, to measure the strength properties and thermal expansion coefficient (Figure 7). Before mechanical processing, the specimens were heat-treated and annealed at 300 °C for 2 hours. Test specimens conforming to GOST 1497-84, Type 3, Part 7, were fabricated from the fabricated cylindrical specimens. Tensile tests were performed on an MTS Criterion 40 universal tensile testing machine in accordance with GOST 1497-84. The thermal expansion coefficient was measured using a DIL 402 Expedis Select dilatometer.

[0043] The mechanical properties and thermal expansion coefficients were determined and are shown in Table 2. The mechanical properties of the prototype materials were not determined due to the impossibility of producing macrocrack-free samples using the selective laser melting technique.

[0044] [Table 2]

[0045] From the data in Tables 1 and 2, it can be seen that the aluminum powder material of the present invention makes it possible to obtain a material without hot cracking / cold cracking in the structure, has high mechanical properties after selective laser melting, and has a coefficient of thermal expansion (CTE) equivalent to that of austenitic stainless steel produced by selective laser melting. [Example]

[0046] A melt was prepared in the crucible of a laboratory furnace, SELT-IPU-15A / 20-NR, using the method described in Example 1. After preparing the melt, the resulting alloy was cast into a steel mold, and the resulting ingot was cut into a size of 50 x 50 x 300 mm. After confirming the chemical composition, the ingot was loaded into the crucible of a vertical atomizer and atomized under a 4.8-grade (99.998%) argon atmosphere. The target particle size of 20–63 μm, D50 = 45 ± 3 μm, was isolated from the resulting atomization. The chemical composition of the resulting powder is shown in Table 3.

[0047] [Table 3]

[0048] From the resulting powder, cube specimens were fabricated to determine the optimal parameters for selective laser melting, as described in Example 1, and cylindrical specimens were fabricated perpendicular to the growth direction.

[0049] The resulting sample blanks were aged at 350 °C for 2, 14, and 20 hours. Test specimens according to GOST 1497-84 Type 3 No. 7 were prepared from the heat-treated sample blanks. Tensile tests were carried out at room temperature according to GOST 1497-84. The mechanical properties were determined and are shown in Table 4.

[0050] [Table 4]

[0051] The data in Table 4 show that the use of long annealing times allows for the achievement of stable mechanical (tensile strength, yield strength) and physical (CTE) properties, allowing the use of the materials of the present invention over a wide operating temperature range without significant degradation of the service properties. The low value of the thermal expansion coefficient of the alloy after annealing for 2 hours indicates that the crystallization of the material during the selective laser melting process is 10 3 -10 6 This is related to the fact that the decomposition process proceeds at a rate of 1000 K / s. This causes the solid solution to become a supersaturated solution, distorting the lattice and lowering the thermal expansion coefficient. Furthermore, because the alloy contains elements that form thermally stable phases, the decomposition process of the supersaturated solid solution proceeds relatively slowly during heat treatment. Figure 8 shows photographs of the microstructure of the alloy after each heat treatment listed in Table 4. [Example]

[0052] Concave and convex mirror products were manufactured from the aluminum powder material obtained in Example 2 using an EOS M 290 machine under the optimal conditions for selective laser melting determined during the implementation of Example 2. The products were heat-treated and annealed at 350 °C for 14 hours. After heat treatment, the products were removed from the build platform and polished. Figure 9 shows the appearance of the platform with the concave and convex mirror blanks. [Example]

[0053] A melt was prepared in the crucible of a laboratory furnace, SELT-IPU-15A / 20-NR, as described in Example 1. After preparing the melt, the resulting alloy was cast into a steel mold, and the resulting ingot was cut into a size of 50 × 50 × 300 mm. After confirming its chemical composition, the ingot was loaded into the crucible of a vertical atomizer and atomized under an atmosphere of argon containing 0.6% oxygen (composition A) and high-purity nitrogen (composition B) of grade 2 in accordance with GOST 9293-74. The target powder particle size (63–150 μm, D50 = 100 ± 5 μm) was isolated from the resulting atomization. The chemical composition of the resulting powder is shown in Table 5.

[0054] [Table 5]

[0055] From the obtained powder, several cubic specimens for porosity measurement and two horizontal specimens were fabricated using direct energy deposition (DED) with an Insstek MX-1000 device at laser powers of 600 W and 700 W and a scanning speed of 850 mm / min, and two specimens for tensile testing were cut from each of these.

[0056] The obtained sample blanks were aged at 350 °C for 14 hours. Tensile tests were carried out at room temperature according to the GOST 1497-84 standard. The mechanical properties and thermal expansion coefficients of the alloys are shown in Table 6.

[0057] [Table 6]

[0058] In this way, various stainless steel products are manufactured using additive manufacturing methods. -6 °С -1 A new aluminum powder material with a low thermal expansion coefficient of 1000 MPa or less and a yield strength of 200 MPa or more was obtained.

[0059] The scope of legal protection claimed is for aluminium powder materials for additive manufacturing techniques containing silicon, nickel, zirconium, chromium, titanium, iron, strontium and / or phosphorus, copper, manganese, magnesium, with the components including aluminium and related impurities as follows: Silicon 33.00 to 45.00 mass% Nickel 1.00 to 3.00 mass% Zirconium 0.10 to 1.00 mass% Chromium 0.10 to 0.80 mass% Titanium 0.05 to 0.50 mass% Iron 0.10 to 0.80 mass% Strontium and / or phosphorus 0.005 to 0.10 mass% Copper 0.02% by mass or less Manganese 0.02% by mass or less Magnesium 0.02% by mass or less

[0060] The powder material preferably has a particle size distribution of 20 to 150 μm and is obtained by gas atomization in a nitrogen or argon atmosphere, and may contain 0.1 to 0.8 mass % of oxygen. -6 °С -1 It has a thermal expansion coefficient of 0.1% or less and a yield strength of 200 MPa or more.

[0061] The scope of the claims also includes a method for manufacturing a product from the aluminum powder material of the present invention using additive manufacturing technology, and a product manufactured from the aluminum powder material using additive manufacturing technology.

Claims

1. An aluminum powder material for additive manufacturing technology containing silicon, nickel, zirconium, chromium, titanium, iron, strontium and / or phosphorus, copper, manganese and magnesium, where the content of each component, including aluminum and related impurities, is as follows: Silicon 33.00 to 45.00 mass% Nickel 1.00 to 3.00 mass% Zirconium 0.10 to 1.00 mass% Chromium 0.10 to 0.80 mass% Titanium 0.05 to 0.50 mass% Iron 0.10 to 0.80 mass% Strontium and / or phosphorus 0.005 to 0.10 mass% Copper 0.02% by mass or less Manganese: 0.02% by mass or less Magnesium 0.02% by mass or less

2. 2. The powder material according to claim 1, characterized in that it has a particle size distribution of 20 to 150 μm.

3. 2. The powder material according to claim 1, characterized in that it is obtained by gas atomization in a nitrogen or argon environment.

4. 2. The powder material according to claim 1, wherein the powder material is obtained by gas atomization in a nitrogen or argon environment with 0.1 to 0.8 mass % of oxygen added.

5. 17・10- 6 °С- 1 2. The powder material according to claim 1, characterized in that it has a thermal expansion coefficient of 0.1% or less and a yield strength of 200 MPa or more.

6. A method for manufacturing a layered object from an aluminum powder material using an additive manufacturing technique, characterized in that the aluminum powder material according to any one of claims 1 to 5 is used to manufacture the layered object.

7. An additively manufactured object made from aluminum powder material using additive manufacturing technology, characterized in that the additively manufactured object is obtained by the manufacturing method described in claim 6 using the powder material described in any one of claims 1 to 5.

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