EP3463718A1

EP3463718A1 - Powder mixture for use in the manufacture of a three-dimensional object by means of an additive manufacturing method

Info

Publication number: EP3463718A1
Application number: EP17725284.8A
Authority: EP
Inventors: Hannu Heikkinen; Antti MUTANEN; Antti PÖRHÖNEN; Maija NYSTRÖM; Tatu Syvänen; Olli Nyrhilä
Original assignee: EOS GmbH
Current assignee: EOS GmbH
Priority date: 2016-06-07
Filing date: 2017-05-26
Publication date: 2019-04-10
Also published as: US20190210103A1; WO2017211602A1; CN109311088A

Abstract

Powder mixture for use in the manufacture of a three-dimensional object by means of an additive manufacturing method, wherein the powder mixture comprises a first material and a second material, wherein the first material comprises a steel in powder form, wherein the second material comprises a reinforcement material different from the first material, and wherein the powder mixture is adapted to form a composite object when solidified by means of an electromagnetic and/or particle radiation in the additive manufacturing method.

Description

POWDER MIXTURE FOR USE IN THE MANUFACTURE OF A THREE-DIMENSIONAL OBJECT BY MEANS OF AN ADDITIVE MANUFACTURING METHOD The present invention relates to a powder mixture for use in the manufacture of a three-dimensional object by means of an additive manufacturing method, a method for the production of the powder-mixture, methods for the manufacture of a three-dimensional object from the powder mixture by selective layer-wise solidification of the powder mixture, a three-dimensional object manufactured from the powder mixture by selective layer-wise solidification, and a control unit for an apparatus for manufacturing a three-dimensional object layer by layer by applying and selectively solidifying the powder mixture.

Examples for additive manufacturing methods, which include also rapid prototyping methods and rapid tooling methods, are known under the names "selective laser sintering" and "selective laser melting". In these methods, a thin layer of building material in powder form is applied repeatedly, and the building material in each layer is selectively solidified at positions corresponding to a cross-section of a three-dimensional object by selective irradiation using a laser beam, i.e. the building material is molten or partially molten at these positions and then solidi- fies.

A method for producing a three-dimensional object by selective laser sintering or selective laser melting as well as an apparatus for carrying out this method are described, for example, in EP 1 762 122 Al . In the article by Dongdong Gu et al . in Applied Surface Science Vol. 255, pages 1880-1887 (published in 2008) the use of stainless steel for laser sintering is disclosed. The properties, especially the mechanical properties, of three-dimensional objects produced from stainless steel, however, are often unsatisfactory .

In order to improve the properties of three-dimensional objects, it is known in the art to produce three-dimensional objects from steel and reinforcement particles, for example silicon carbide particles, by means of conventional sintering methods and casting methods. The reinforcement effect, however, is limited, for example, due to the dissolution of the reinforcement particles in the molten iron during the processing time.

An object of the present invention is to provide a powder mixture, the use of which makes improved additive manufacturing methods available, a method for the production of such a powder mixture, improved methods for the manufacture of a three-dimen- sional object making use of the powder mixture, an improved three-dimensional object manufactured from the powder mixture, for example a three-dimensional object with improved mechanical properties, and a control unit for an apparatus for manufacturing a three-dimensional object making use of the powder mixture.

The object is achieved by the powder mixture according to claim 1, the method for the production of a powder mixture according to claim 13, the methods for the manufacture of a three-dimensional object according to claims 14 and 21, the three-dimen- sional object according to claim 16, and the control unit according to claim 20. Refinements of the invention are specified in the dependent claims. Any feature set forth in the dependent claims as well as any feature set forth in the description of exemplary embodiments of the invention below can be understood as a feature suitable for refining the powder mixture, the method for the production of a powder mixture, the methods for the manufacture of a three-dimensional object, the three-dimen- sional object, and the control unit.

A powder mixture is understood as a granular mixture of two or more components. The powder mixture according to the invention comprises a first and a second material. The second material comprises a reinforcement material. The powder mixture is for use in an additive manufacturing method. The so manufactured three-dimensional objects comprise composite materials. A composite material is a material with a matrix material in which a reinforcement material is embedded. Composite materials often have improved (mechanical) properties compared to the matrix material and/or the reinforcement material.

The powder mixture according to the invention is a powder mixture for use in the manufacture of a three-dimensional object by means of an additive manufacturing method, wherein the powder mixture comprises a first material and a second material, wherein the first material comprises a steel in powder form, wherein the second material comprises a reinforcement material different from the first material, and wherein the powder mix- ture is adapted to form a composite object when solidified by means of an electromagnetic and/or a particle radiation in the additive manufacturing method. The first and/or the second material may comprise further materials. Using this powder mixture, for example improved additive manufacturing methods, especially additive manufacturing methods leading to three-dimensional objects comprising a composite material with improved properties compared to the pure matrix material, are provided. Preferably, the reinforcement material is embedded in a matrix of the composite object at least partially in a chemically unmodified form. This means that at least a part of the reinforcement material being comprised by the second material does not undergo a change of its chemical composition prior to being embedded in the matrix.

The steel preferably contains Fe and max 0.10 wt% C, 2.00 - 3.00 wt% Mo, 10.00 - 15.00 wt% Ni, and 16.00 - 19.00 wt% Cr; more preferably, it further contains max 0.030 wt% S, max

0.045 wt% P, max 0.16 wt% N, max 0.50 wt% Cu, max 1.00 wt% Si, and max 2.00 wt% Mn.

Preferably, the median grain size of the first material is 1 μιη or more, more preferably 5 μπι or more, still more preferably 10 μτη or more, and/or 150 μπι or less, more preferably 75 μιη or less .

Preferably, the particles of the first material are substan- tially spherical.

Preferably, the reinforcement material comprises at least one non-metallic material, wherein more preferably the non-metallic material is one out of borides and carbides and nitrides and ox- ides and silicides and graphite.

Preferably, the reinforcement material comprises silicon carbide, wherein more preferably the reinforcement material is silicon carbide .

Preferably, the reinforcement material comprises titanium carbide, wherein more preferably the reinforcement material is titanium carbide . Preferably, the reinforcement material comprises tungsten carbide, wherein more preferably the reinforcement material is tungsten carbide.

Preferably, the reinforcement material is a powder, wherein the median grain size of the reinforcement material is 0.5 μηα or more, preferably 1 μιτι or more. Preferably, the median grain size of the reinforcement material is 100 μιτι or less, preferably 50 μπι or less.

Preferably, the particles of the reinforcement material have a substantially spherical or a substantially angular or a substan- tially irregular shape.

Preferably, the content of the reinforcement material in the powder mixture is 0.05 wt% or more, preferably 0.1 wt% or more, more preferably 0.3 wt% or more, still more preferably 0.5 wt% or more.

Preferably, the content of the reinforcement material in the powder mixture is 40 wt% or less, preferably 10 wt% or less, more preferably 5 wt% or less, still more preferably 4 wt% or less. For example, if the reinforcement material comprises tungsten carbide, the content of the reinforcement material is particularly preferably 40 wt% or less, even more preferably 10 wt% or less. The method for the production of a powder mixture according to the invention is a method for the production of a powder mixture for use in the manufacture of a three-dimensional object by means of an additive manufacturing method, wherein the powder mixture comprises a first material and a second material, wherein the first material comprises a steel in powder form, wherein the second material comprises a reinforcement material different from the first material, and wherein the powder mix- ture is adapted to form a composite object when solidified by- means of an electromagnetic and/or a particle radiation in the additive manufacturing method, wherein the powder mixture is produced by mixing the first material and the second material in a predetermined mixing ratio. Using this method, a powder mix- ture according to the invention can be produced.

Preferably, the mixing is a dry mixing.

A method for the manufacture of a three-dimensional object ac- cording to the invention is a method for the manufacture of a three-dimensional object from a powder mixture by selective layer-wise solidification of the powder mixture by means of an electromagnetic radiation and/or a particle radiation at positions that correspond to a cross-section of the object in a re- spective layer, wherein the powder mixture is a powder mixture for use in the manufacture of a three-dimensional object by means of an additive manufacturing method, wherein the powder mixture comprises a first material and a second material, wherein the first material comprises a steel in powder form, wherein the second material comprises a reinforcement material different from the first material, and wherein the powder mixture is adapted to form a composite object when solidified by means of an electromagnetic and/or a particle radiation in the additive manufacturing method. Using this method, for example a three-dimensional object with improved material properties can be manufactured. Preferably, the method for the manufacture of a three-dimensional object comprises the steps:

applying a layer of the power mixture on the base plate or on the building platform or on a previously applied layer,

solidifying the powder mixture selectively at positions corresponding to a cross - section of the three-dimensional object in the layer, and

repeating the steps of applying and solidifying until the three-dimensional object is completed.

The three-dimensional object according to the invention is a three dimensional object manufactured from a powder mixture by selective layer-wise solidification of the powder mixture by means of an electromagnetic and/or particle radiation at posi- tions that correspond to a cross - section of the object in a respective layer, wherein the powder mixture is a powder mixture for use in the manufacture of a three-dimensional object by means of an additive manufacturing method, wherein the powder mixture comprises a first material and a second material, wherein the first material comprises a steel in powder form, wherein the second material comprises a reinforcement material different from the first material, and wherein the powder mixture is adapted to form a composite object when solidified by means of electromagnetic and/or particle radiation in the addi- tive manufacturing method. The three-dimensional object has, for example, improved mechanical properties and/or improved corrosion properties and/or an improved balance between these properties compared to a three-dimensional object manufactured from the first material.

Preferably, the reinforcement material is embedded in a matrix of the composite object at least in a chemically unmodified form. Preferably, the material of the three-dimensional object has a tensile strength of 500 MPa or more, more preferably 800 MPa or more, most preferably 900 MPa or more.

Preferably, the material of the three-dimensional object has a yield strength of 170 MPa or more, preferably 400 MPa or more, most preferably 600 MPa or more. If the reinforcement material comprises tungsten carbide, thema- terial of the three-dimensional object has a tensile strength of 500 MPa or more, more preferably 750 MPa or more, most preferably 1000 MPa or more. If the reinforcement material comprises tungsten carbide, the material of the three-dimensional object has a yield strength of 200 MPa or more, preferably 500 MPa or more, most preferably 800 MPa or more . Preferably, a reduction of a pin mass loss in wear testing of the three-dimensional object compared to a pin mass loss in wear testing of a three-dimensional object manufactured from the first material by selective layer-wise solidification of the first material by means of the electromagnetic and/or particle radiation at positions that correspond to a cross-section of the object in a respective layer is 25% or more, preferably 50% or more, more preferably 75% or more.

Preferably, an increase of a disk mass loss in wear testing of the three-dimensional object compared to a disk mass loss in wear testing of a three-dimensional object manufactured from the first material by selective layer-wise solidification of the first material by means of the electromagnetic and/or particle radiation at positions that correspond to a cross-section of the object in a respective layer is 15% or more, preferably 50% or more, more preferably 70% or more. The control unit according to the invention is a control unit for an apparatus for manufacturing a three-dimensional object layer by layer by applying and selectively solidifying a powder mixture, wherein the powder mixture is a powder mixture for use in the manufacture of a three-dimensional object by means of an additive manufacturing method, wherein the powder mixture comprises a first material and a second material, wherein the first material comprises a steel in powder form, wherein the second material comprises a reinforcement material different from the first material, wherein the powder mixture is adapted to form a composite object when solidified by means of an electromagnetic and/or a particle radiation in the additive manufacturing method, and wherein the control unit is adapted to control that a predefined amount of energy is introduced into a defined volume of the powder mixture by means of the electromagnetic and/or particle radiation. This, for example, provides a control unit for an apparatus for manufacturing a three-dimensional object with improved material properties .

Preferably, an upper limit of the predefined amount of energy is selected such that the reinforcement material is not completely dissolved during the time in which the predefined amount of energy is applied to the defined volume of the powder mixture.

Preferably, the upper limit of the predefined amount of energy is defined such that the reinforcement material of the powder mixture is dissolved to 70 wt% or less, preferably 50 wt% or less, more preferably 30 wt% or less, even more preferably 5 wt% or less during the time in which the predefined amount of energy is applied to the defined volume of the powder mixture.

A method for the manufacture of a three-dimensional object ac- cording to the invention is a method for the manufacture of a three-dimensional object from a powder mixture by selective layer-wise solidification of the powder mixture by means of an electromagnetic and/or a particle radiation at positions that correspond to a cross-section of the object in a respective layer, wherein the powder mixture comprises a first material and a second material, wherein the first material comprises a metal in powder form, wherein the second material comprises a reinforcement material, wherein the powder mixture is selectively solidified by means of an electromagnetic and/or a particle ra- diation at positions that correspond to a cross-section of the object in a respective layer forming a composite material, and wherein 90 wt% or less, preferably 70 wt% or less, more preferably 50 wt% or less, still more preferably 30 wt% or less, even more preferably 5 wt% or less of the reinforcement material are dissolved in the metal. Using this method, for example a three- dimensional object with improved material properties can be manufactured .

Other features and expediencies of the invention may be found in the description of exemplary embodiments with the aid of the appended drawings .

Fig. 1 is a schematic view, partially represented in section, of an apparatus for the layer-wise manufacture of a three-dimensional object according to an embodiment of the present invention. Fig. 2 shows FE-SEM images of the first and the second material used to produce a powder mixture according to an embodiment of the invention. Fig. 3 shows BSE FE-SEM images of two powder mixtures according to this embodiment of the invention.

Fig. 4 shows the measured density and the calculated theoretical density for three examples according to this embod- iment of the invention.

Fig. 5 shows the measured tensile and yield strength and their standard deviations for these three examples. Fig. 6 shows the measured hardness together with its standard deviation for these three examples.

Fig. 7 shows the pin mass loss and the disk mass loss measured by wear testing for these three examples .

Fig. 8 shows a FE-SEM image of the second material used to

produce a powder mixture according to another embodiment of the invention. Fig. 9 shows a FE-SEM image of the first material used to produce a powder mixture according to this embodiment.

Fig. shows the measured density, the calculated theoretical density and the relative density of four examples of solid material samples according to this embodiment. Fig. 11 shows a FE-SEM image of Tie particles in the composite structure of manufactured three-dimensional objects according to this embodiment . Fig. 12 shows the tensile strength and yield strength as well as the elongation after fracture for the four examples for which data are shown in Fig. 10.

Fig. 13 shows the tensile strength and yield strength as well as the impact energy for these four examples.

Fig. 14 shows the pin mass loss measured by wear testing for these four examples . Fig. 15 shows the hardness measured for these four examples.

Fig. 16 shows a FE-SEM image of the second material used to

produce a powder mixture according to another embodiment of the invention.

Fig. 17 shows the measured density, the calculated theoretical density and the relative density of four examples of solid material samples according to this embodiment. Fig. 18 shows a FE-SEM image of WC particles in the composite structure of manufactured three-dimensional objects according to this embodiment.

Fig. 19 shows the tensile strength and yield strength as well as the elongation after fracture for the four examples for which data are shown in Fig. 17. Fig. 20 shows the pin mass loss measured by wear testing for two of these four examples .

Fig. 21 shows the hardness measured for these four examples.

The apparatus represented in Fig. 1 is a laser sintering or laser melting apparatus 1 for the manufacture of a three-dimensional object 2. The apparatus 1 contains a process chamber 3 having a chamber wall 4. A container 5 being open at the top and having a container wall 6 is arranged in the process chamber 3. The opening at the top of the container 5 defines a working plane 7. The portion of the working plane 7 lying within the opening of the container 5, which can be used for building up the object 2, is referred to as building area 8. Arranged in the container 5, there is a support 10, which can be moved in a vertical direction V, and on which a base plate 11 which closes the container 5 toward the bottom and therefore forms the base of the con- tainer 5 is attached. The base plate 11 may be a plate which is formed separately from the support 10 and is fastened on the support 10, or may be formed so as to be integral with the support 10. A building platform 12 on which the object 2 is built may also be attached to the base plate 11. However, the object 2 may also be built on the base plate 11, which then itself serves as the building platform.

In Fig. 1, the object 2 to be manufactured is shown in an inter mediate state. It consists of a plurality of solidified layers and is surrounded by building material 13 which remains unsolid The apparatus 1 furthermore contains a storage container 14 for building material 15 in powder form, which can be solidified by electromagnetic radiation, for example a laser, and/or particle radiation, for example an electron beam. The apparatus 1 also comprises a recoater 16, which is movable in a horizontal direction H, for applying layers of building material 15 within the building area 8. Optionally, a radiation heater 17 for heating the applied building material 15, e.g. an infrared heater, may be arranged in the process chamber.

The apparatus 1 furthermore contains an irradiation device 20 having a laser 21, which generates a laser beam 22 that is deflected by means of a deflecting device 23 and focused onto the working plane 7 by means of a focusing device 24 via an entrance window 25, which is arranged at the top side of the process chamber 3 in the chamber wall 4.

The apparatus 1 furthermore contains a control unit 29, by means of which the individual component parts of the apparatus 1 are controlled in a coordinated manner for carrying out a method for the manufacture of a three-dimensional object. The control unit 29 may contain a CPU, the operation of which is controlled by a computer program (software) . During operation of the apparatus 1, the following steps are repeatedly carried out: For each layer, the support 10 is lowered by a height which preferably corresponds to the desired thickness of the layer of the building material 15. The recoater 16 is moved to the storage container 14, from which it receives an amount of building material 15 that is sufficient for the application of at least one layer. The recoater 16 is then moved over the building area 8 and applies a thin layer of the building material 15 in powder form on the base plate 11 or on the building platform 12 or on a previously applied layer. The layer is applied at least across the cross-section of the object 2, preferably across the entire building area 8. Optionally, the building material 15 is heated to an operation temperature by means of at least one radiation heater 17. The cross-section of the object 2 to be manufactured is then scanned by the laser beam 22 in order to selectively solidify this area of the applied layer. These steps are carried out until the object 2 is completed. The object 2 can then be removed from the container 5.

According to the invention, a powder mixture is used as building material 15. The powder mixture comprises a first material and a second material. According to the embodiments described below, the first material comprises a steel in powder form. The second material comprises a reinforcement material.

According to the embodiments described below, the powder mixture is processed by the direct metal laser sintering (DMLS) method. In the selective laser sintering or selective laser melting method small portions of a whole volume of powder required for manufacturing an object are heated up simultaneously to a temperature which allows a sintering and/or melting of these portions. This way of manufacturing an object can typically be characterized as a continuous and/or - on a micro-level - frequently gradual process, whereby the object is acquired through a multitude of heating cycles of small powder volumes. Solidification of these small powder portions is carried through selectively, i. e. at selected positions of a powder reservoir, which positions correspond to portions of an object to be manufactured. As in selective laser sintering or selective laser melting the process of solidification is usually carried through layer by layer the solidified powder in each layer is identical with a cross-section of the object that is to be built. Due to the small volume or mass of powder which is solidified in a given time span, e. g. 1 mm³ per second or less, and due to conditions in a process chamber of such additive manufacturing ma- chines, which can favour a rapid cool-down below a critical temperature, the material normally solidifies quickly after heating.

In conventional sintering and casting methods one and the same portion of building material is heated up to a required temperature at the same time. A whole portion of material required to generate an object is cast into a mould in a liquid form. This volume of building material is therefore held above a temperature level required for melting or sintering for a much longer time compared to the selective laser sintering or selective laser melting method. Large volumes of hot material lead to a low cooling rate and a slow solidification process of the building material after heating. In other words, selective laser sintering or selective laser melting methods can be differentiated from conventional sintering and casting methods by processing of smaller volumes of building material, faster heat cycles and less need for heating up build material with high tolerances for avoiding a premature solidification of the material. These can be counted among the reasons why the amount of energy introduced into the building material for reaching the required temperatures can be controlled more accurately in selective laser sintering or selective laser melting methods. These conditions allow for setting an upper limit of energy input into the powder portions to be processed, which determines a temperature generated in the powder portions, more precisely, that is lower and closer to the melting point of the respective material than in conventional sintering or casting methods. This advantage makes it possible to minimize common problems of conventional sintering and casting methods. One such phenomenon is dissolution of reinforcement material in a steel melt during manufacturing, especially if a resulting composite material is thermodynamically unstable. The selective laser sintering or selective laser melting method allows for reducing dissolution by lowering the heating temperatures, for example generated by a laser and/or electron beam, in defined areas of the powder bed and for raising a cooling rate after heating. Thus, the reinforcing quality of the reinforcement material, i.e. its ability to change (mechanical) properties of an object in a favourable manner, can become much more apparent. The phrase "mechanical properties of an object" is understood in this context as properties which derive from mate- rial properties of the object and not from a specific shape and/or geometry of the object. Mechanical properties of the object can be tensile strength or yield strength, for example. An object generated from a powder mixture according to the invention may show a change of various mechanical properties . The in- ventive method of manufacturing a three-dimensional object provides considerable advantages by improving selected mechanical properties compared to an object manufactured without reinforcement material . A comparatively short exposure of the building material or the formed composite material to high temperatures leads to a minimization of the dissolution of the reinforcement material in the first material. Furthermore chemical reactions of the reinforcement material with the first material are minimized. This is im- portant as the reaction products are generally brittle. If the layer of the reaction product is thick, a considerable weakening of the material can occur. In the case of stainless steel, the reactions can also lead to a depletion of free chromium in the structure surrounding the reinforcement particles and a loss of corrosion resistance in these areas .

In a specific embodiment of the invention, the first material is a 316L grade steel according to the SAE steel grade system

(hereinafter referred to as "316L") . This steel contains Fe and up to 0.03 weight percent (wt%) carbon, up to 0.10 wt% nitrogen, up to 0.50 wt% copper, up to 0.75 wt% silicon, up to 2.00 wt% manganese, between 2.25 and 3.00 wt% molybdenum, between 13.00 and 15.00 wt% nickel, and between 17.00 and 19.00 wt% chromium.

The steel is used as a powder with substantially spherically shaped powder particles, which means that at least most of the powder particles have a high sphericity.

The steel particles can have a regularly rounded shape and/or a smooth surface but they can also have areas with a rough surface and other deviations. The powder has a median grain size (d50- value) between 33 and 40 μτη. The material is, e.g., obtainable from EOS GmbH Electro Optical Systems under the tradename "EOS StainlessSteel 316L" .

The term "median grain size", also denoted as "d50-value", is understood as the particle diameter corresponding to the median of a particle volume distribution. The median grain size can be determined by means of laser scattering or laser diffraction.

The second material is silicon carbide (SiC) powder according to this embodiment. The median grain size (d50-value) of the sili- con carbide powder particles lies between 25 and 35 μτ . The silicon carbide powder particles have a substantially angular shape, i.e. at least most of the powder particles have edges and vertices. Preferably, they do not have cavities but they can have concave portions. Preferably, they are not elongated particles. The material is, e.g., obtainable from the Compagnie de Saint-Gobain under the tradename "SIKA ABR I F320". The particle size distribution of this material is measured according to FEPA Standard 42-1:2006 for Macro-, and 42-2:2006 for Micro-Grains.

In Fig. 2 FE-SEM images of the 316L powder (left image) and the silicon carbide powder (right image) are shown. The images show that the particles of the 316L powder have a substantially spherical shape and that the particles of the silicon carbide powder have an angular shape .

FE-SEM imaging has been done using Zeiss ULTRAplus FE-SEM system equipped with two separate secondary electron (SE) detectors and a back scattered electron (BSE) detector. A small amount of each sample powder has been spread evenly on a piece of electrically conductive carbon tape and mounted to a sample holder. Images have been captured with 100X magnification using the BSE imaging mode and 15.00 kV acceleration voltage of the electron beam.

Alternatively, a steel of a different type can be used as first material, for example a maraging steel, for example X3Ni- CoMoTil8-9-5 (classification according to DIN EN 10027-1) , which is, e.g., obtainable from EOS GmbH Electro Optical Systems under the tradename "EOS MaragingSteel MSI".

Alternatively, the second material can comprise a reinforcement material with substantially spherical particles. It can also comprise a reinforcement material with irregularly shaped parti- cles, e.g. with elongated particles having an aspect ratio up to Alternatively, the reinforcement material can be a material different from silicon carbide.

It is generally preferred that the reinforcement material has a higher melting point than the steel of the first material. If the powder mixture according to the invention is heated to a temperature where the steel powder melts, the reinforcement material can remain solid, for example in crystalline form, if the temperature is held below the melting point of the reinforcement material. A composite object manufactured by this method can thus gain particularly favourable properties, for example mechanical properties.

Titanium carbide, tungsten carbide, other carbides, borides, ni- trides, oxides, silicides, graphite, and other non-metallic materials with high melting points, especially ceramics, can be selected as reinforcement materials.

According to this embodiment, the powder mixture is produced by mixing the 316L powder and the silicon carbide powder using a dry mixing process with a uniaxial rotating mixer. The powder components are weighed and sealed in a cylindrical glass jar. The jar is rotated with a rotational speed of 15 rpm for 20 minutes. The selected rotational speed allows the powder to flow to the opposite end of the partially filled jar during each revolution in order to ensure that the silicon carbide becomes dispersed in the steel powder. The selected mixing time ensures that the silicon carbide becomes dispersed in the steel powder and that the accumulation of electrostatic forces within the mixture is minimized. Using this mixing method a homogenous powder mixture is obtained. This means that the silicon carbide particles may be distributed evenly in the 316L particles so that substantially the same mixing ratio (number of particles and/or weight percent) can be measured in any portion of powder mixture of a certain volume and/or weight .

The powder mixture according to this embodiment is used as building material for manufacturing three-dimensional objects by selective laser sintering or selective laser melting using the EOS M100 DMLS-system having a Yb fibre laser as laser sintering or laser melting apparatus 1.

The manufactured three-dimensional objects consist of a composite material made up of a matrix being at least predominantly a steel matrix with SiC reinforcement particles.

The process parameters of the selective laser sintering or selective laser melting process are preferably selected such that the amount of energy that is introduced into a defined volume of the powder mixture by an electromagnetic radiation (for example a laser) and/or a particle radiation (for example an electron beam) is equal to or below a predefined upper limit. The upper limit is predefined such that it is ensured that the reinforcement material is not completely dissolved in the melt of the first material during the time in which the electromagnetic radiation and/or particle radiation heats the defined volume. The power of a laser or electron beam, for example, as a main determining factor of the heat generated in a powder portion can be controlled by means of a control unit as part of the additive manufacturing machine. The control unit can be connected to a database, wherein correlations between process parameters are stored, and concrete values, for example a power input for the laser or electron beam, are generated based on predefined parameters or thresholds. These values can be fed into the control unit which generates control signals for adjusting a power of a laser or electron beam as part of the additive manufacturing machine correspondingly. The control unit can also work based on sensor data of an active process monitoring system which detects if a heating and/or solidifying process runs within specified operational parameters .

Reinforcement material is said to be dissolved if its structural elements detach from the reinforcement material structure and spread in a first material, regardless of whether a chemical re- action of the reinforcement material and the first material takes place. The amount of the reinforcement material that is dissolved is preferably 70 wt% or less, more preferably 50 wt% or less, still more preferably 30 wt% or less, and still more preferably 5 wt% or less. The control unit 29 of the laser sin- tering or melting apparatus 1 can be adapted to control the apparatus 1 such that the amount of energy that is introduced into a defined volume of the powder mixture by means of electromagnetic radiation and/or particle radiation is equal to or below the upper limit.

The process parameters of the selective laser sintering or selective laser melting process are preferably selected such that the amount of energy that is introduced into a defined volume of the powder mixture by means of electromagnetic radiation and/or particle radiation is equal to or above a predefined lower limit. The lower limit is predefined such that it is ensured that the first material is completely molten during the time in which the electromagnetic radiation and/or the particle radiation introduces energy into the defined volume of the powder mixture, whereby the energy input can be controlled by a control unit which can work depending on data provided by a database and/or by an active process monitoring system. The control unit 29 of the laser sintering or melting apparatus 1 can be adapted to control the apparatus 1 such that the amount of energy that is introduced into a defined volume of the powder mixture by means of the electromagnetic radiation and/or the particle radiation is equal to or above the lower limit.

Partial dissolution of the reinforcement material in the melt of the first material or reaction of the reinforcement material with the first material can actually be beneficial as it can improve the bonding between the reinforcement material and the steel, which in turn improves the load transfer from the first material to the reinforcement material. Without load transfer, the reinforcement material could not contribute to the strength properties of the material. Dissolution of the reinforcement material in the melt of the first material/reaction of the rein- forcement material with the first material is typically the problem with conventional sintering and casting methods. Therefore, it can be necessary to find a compromise between bond strength and dissolution of the reinforcement material in the melt of the first material/reaction of the reinforcement mate- rial with the first material. In this instance, the lower limit for the amount of energy that is introduced into a defined volume of the powder mixture can be selected such that it is ensured that the reinforcement material is partially dissolved in the melt of the first material during the time in which the electromagnetic radiation and/or the particle radiation introduces energy into the defined volume, wherein the amount of the reinforcement material that is dissolved is preferably 1 wt% or more, more preferably 3 wt% or more. The process parameters which can be changed in order to control the amount of energy that is introduced into a defined volume of the powder mixture are, for example, laser spot size, laser beam profile, laser output power (radiant energy that can, for example, be transmitted through an optical system before it is actually used in the process) , thickness of a powder layer, distance between individual scanning lines of, for example, a laser or electron beam, and scanning speed of, for example, a laser or electron beam over the predefined areas to be solidified. One has to take account of the possible interdependence of some of these parameters. For example, for a given laser beam profile, for instance a Gaussian beam profile, and a given beam diameter, the hatch distance can lie between an upper limit and a lower limit in order to ensure that the energy input into the building material is sufficient at all positions to be solidified without overheating the building material and without leaving a sintering or melting process incomplete .

Also increased porosity caused by the reinforcement material may be a reason for unsuccessful strengthening using conventional sintering and casting methods. This problem can be avoided using selective laser sintering or selective laser melting methods.

The process parameters of the selective laser sintering or selective laser melting process are preferably selected such that the heat input factor Q and the spot size of the laser lie within certain preselected ranges in order to ensure that the first material is sufficiently molten and to avoid a complete dissolution of the reinforcement material in the first material. The heat input factor should lie within these ranges independently of other parameters, for example a spot size of the laser on the powder bed, which may vary according to different angles under which a laser beam reaches different positions in the building area 8 in which single powder portions are to be solidified. The heat input factor is an approximate measure for the amount of energy that is introduced into a defined volume of the powder mixture by means of the laser beam. More specifically, the heat input factor is a measure for the amount of energy introduced per volume of the powder mixture. It is, for example, measured in units of J/mm³. The heat input factor Q is calculated based on the laser output power P, the hatch distance d, the hatch speed v, and the layer thickness s according to the formula

Q = P / (d * v * s)

It has been found out that a heat input factor lying between 30 and 150 J/mm³ and a spot size of the laser lying between 35 and 120 μπι lead to three-dimensional objects having favourable properties, for example favourable mechanical properties.

The following values have been found out to be very favourable process parameters in cases where silicon carbide is used as reinforcement material: P = 105 W, d = 0.07 mm, v = 830 mm/s, s = 0.02 mm. These values correspond to Q = 90.4 J/mm³. These pa- rameters have been used for the manufacture of three-dimensional objects using the mixtures A, B, and C to be described below.

The three-dimensional objects manufactured by means of the method according to the embodiment of the invention described above are characterized with respect to various properties. The methods used for the characterization are described below.

1. Densities are determined utilizing the Archimedes' principle according to standard ISO 3369: "Impermeable sintered metal materials and hard metals - Determination of density" for three- dimensional objects manufactured as density cube samples by selective laser sintering or selective laser melting are used for density testing. In this density testing method, the mass of a sample is determined both in air and as immersed in water, and the measured mass difference between the two measurements is then used for the estimation of the sample volume based on the known density of water. From the measured weight and volume of the sample, its density can then be calculated. For the tests, all sides of the density cube samples are ground manually with Struers SiC #320 abrasive paper using Struers Labo-Pol-5 sample preparation system in order to reduce the surface roughness and thereby the possibility of test result deterioration due to trapped air bubbles on the sample surfaces. Ion-exchanged water is used for the weighing in water immersion, and a small amount of dish washing liquid is added to the water in order to lower its surface tension. The procedure is performed with a laboratory scale (Kern PLT 650 -3M) using an inbuilt density calcula- tion program. For the automated calculation, the water temperature is measured before the tests. The measurements are repeated three times for each sample switching the sample between each measurement, and before each new measurement the samples are dried thoroughly. The results presented below are the averaged values of the three measurements.

Due to the significantly lower density of silicon carbide in comparison to the selected first material, some extent of density decrease can be expected to be related to the increasing silicon carbide content of the samples. In order to evaluate the effect of silicon carbide addition on the structural integrity of the materials, this direct density reduction effect is calculated and the theoretical composite material densities are compared to the measured density values . The calculations are based on the theoretical density of solid silicon carbide (3.21 g/cm³) and the measured density of a sample manufactured from 316L without reinforcement material (7.99 g/cm³). These densities are used for estimating the volume fraction of silicon carbide in the materials. Then, based on these theoretical volume fractions and the stated densities of the solid material constituents, the theoretical densities of the solid composite materials are calculated. The described procedure can be expressed by the equa- tions

SiC volume fraction = SiC wt% / SiC density / (SiC wt% / SiC density + 316L wt% / 316L density) 316L volume fraction = 316L wt% / 316 L density / (SiC wt% / SiC density + 316L wt% / 316L density) composite density = SiC volume fraction * SiC density + 316L volume fraction * 316L density

It is clear from the equations, that these theoretical composite densities are based on the assumption that the silicon carbide particles do not add any empty volume to the composite material structure, and that the same level of defects that was present in the original 316L sample would be present also in the composite materials.

2. Tensile testing is carried out according to standard ISO 6892-1 : 2009 : B10 "Metallic materials - Tensile testing - Part 1: Method of test at room temperature". Three-dimensional objects manufactured as tensile test pieces (samples) by selective laser sintering or selective laser melting are used for tensile testing. The cross-section diameter of each sample is reduced with a turning lathe so that it reaches its smallest value, approxi- mately 4.0 mm, in the middle of the samples. This diameter is verified with a micrometre. The ends of the samples are threaded for fastening. The testing is done with Zwick/Roell Z400-test machine (Zwick Roell Group) . The tensile force is increased by 10 MPa/s during the elastic phase of the material behaviour, and the increase is reduced to 0.375 MPa/s at the beginning of the plastic deformation phase. During the tests, the maximum load, offset yield strength (R_p0.2- limit) , tensile strength, and elon- gation of the samples at fracture are recorded, and the reduction of the cross-section area at the point of fracture is then measured with a slide.

3. In the case of this embodiment, hardness testing of the three-dimensional objects manufactured as samples by selective laser sintering or selective laser melting is carried out using the Rockwell method. The tests are performed according to the standard EN-ISO 6508-1:2005 "Metallic materials - Rockwell hardness test - Part 1: Test method". Density cube samples are used for the testing. The tests are performed five times for each sample, and the measured values are reported with an accuracy of 0.1 HRB. In the Rockwell test method, an indenter of a specified shape, dimensions and material is pressed against the sample surface with a defined force through a two-step procedure. The force is applied by adding a specified load on the indenter. First, the indenter is pressed with a small preliminary force and the resulting initial indentation depth is measured, after which a greater additional force is applied and then removed. After returning to the preliminary force level, the final inden- tation depth is measured and the hardness of the sample is calculated based on the difference in the depths of the initial and final indentations through the equation

Hardness = N - h/s, where h is the measured difference in the indentation depths and N and s are scale-specific constants specified in the standard. The standard also specifies the type of the indenter, and its shape and material are varied depending on the hardness of the test material. The test procedure deviates from the standard in that a tungsten carbide (WC) ball indenter is used also when hardness values of over 100 HRB are measured, instead of a dia- mond cone as specified in the standard. This deviation could lead to an increased measurement error due to shape deformation of the indenter and small depth of the indentation. However, as the 100 HRB hardness limit is not significantly exceeded in the present case, these factors are not assumed to influence the test results to a high extent. The tungsten carbide ball indenter used in the tests has a diameter of 1.5875 mm (1/16 inch), and the applied preliminary and total forces were 98.07 N and 980.70 N, respectively, corresponding to applied loads of 10.0 kg and 100.0 kg .

4. Resistance to abrasive wear is tested by the ball-on-disk - method according to the standard ASTM G99 - 95a "Standard Test Method for Wear Testing with a Pin-on-Disk Apparatus" . In this method, a pin specimen with a spherical head is pressed perpen- dicularly against a horizontally rotating disk of a pre-defined material and surface finish. The pin sliding speed and sliding distance, as well as the normal force between the contacting surfaces are also to be defined in the testing setup. The tests are performed at room temperature. After the tests, the material analysis is performed based on the mass or volume loss of the pin and disk specimens, contact surface characterization and the frictional force data recorded during the tests using CETR UMT-2 tribometer . The tests are performed using disk specimens made of maraging steel powder EOS MaragingSteel MSI manufactured by selective laser sintering or selective laser melting using the EOS M290 DMLS-system having a Yb fibre laser and default process parameters provided by the manufacturer of the EOS M290 DMLS-system. The test surfaces of the disk specimens are ground manually with Struers SiC #80 and #320 abrasive papers in the respective order by Struers LaboPol-5 sample preparation system. The surface roughness values of the samples are measured with a surface roughness tester (Mitutoyo Surftest SJ-210) , and the measurements are repeated four times from different positions of each disk. The measured roughness values are typically in the order of 1 μιη in the present case.

5. Corrosion resistance of three-dimensional objects manufactured as samples by selective laser sintering or selective laser melting is tested according to the standard NACE TM0169/G31 - 12a "Standard Guide for Laboratory Immersion Corrosion Testing of Metals". The test period is set to 30 days, after which the test results are evaluated by visual inspection and sample mass change measurement. All sample surfaces are first ground manually with Struers SiC #80 and #320 abrasive papers using Struers LaboPol-5 sample preparation system. The samples are then let to oxidize in the room atmosphere for 24 hours in order to simulate the probable real-life operating conditions of the test materials. The samples are then cleaned first by scouring them with paper and ethanol and then by rinsing in an ultrasonic bath (Retsch UR1, Retsch GmbH) for 5 minutes, using ion-exchanged water. The sample dimensions are then measured with a slide caliper (ABSOLUTE AOS Digimatic Caliper 500-123U, Mitutoyo UK Ltd) in order to determine their surface areas, and they are weighed with a laboratory scale (Kern PLT 650-3M) . The tests are per- formed in a standard sea water environment, in which the electrolyte is a mixture of ion-exchanged water and 3.56 wt% reagent-grade sodium chloride (NaCl, Baker Analyzed, J.T. Baker) . The solution is prepared by measuring 900g of the water and 33.22g NaCl separately with a laboratory scale (Kern PLT 650-3M) and combining them in plastic test containers. The dissolution of NaCl is agitated by rotating the containers manually for 30 seconds. The containers are made of high-density polyethylene (PE-HD) and have a volume of 1000 ml. The samples are attached to the lid of the containers with polymer strings so that they are positioned roughly in the middle of the containers in vertical direction. The samples are not allowed to come in contact with the container walls during the tests. The tests are carried out at room temperature (20-25°C) and ambient pressure. After 30 days the samples are rinsed and cleaned following a two-step procedure. In the first step, they are rinsed in ion-exchanged water and blow dried, and in the second step they are brushed under ion-exchanged water with an electric tooth brush and then rinsed in an ultrasonic bath for three minutes . The samples are weighed three times after each cleaning step with a laboratory scale (Kern PLT 650-3M) .

Assuming that the corrosion on the sample surfaces advances with a uniform rate on the whole surface area, the rate of uniform corrosion penetration can be estimated based on the measured weight losses and the known sample surface areas. The calculations are performed by the equation Rate of uniform corrosion penetration = (K * W) / (A * T * D) , in which K is a measurement unit-specific constant with a value of 8.76 * 10⁴ for the calculation of the rate of uniform corrosion penetration as millimeters per year (mm/yr) , W is the sam- pie mass loss in grams, A is the sample surface area in cm², T is the time of exposure in hours and D is the sample material density. For the wear testing, three-dimensional objects are manufactured as pin specimens by selective laser sintering or selective laser melting. No additional surface treatment is done. The following parameters have been chosen for the tests: Normal force = 40.0 N, sliding speed = 0.25 m/s, sliding distance = 450.0 m, test time = 30.0 min. Due to the slight unevenness of the disk sample surfaces, the normal force value may thereby fluctuate by approximately 5.0 N from the pre-set value during each disk revolution. This extent of normal force fluctuation is typical for the described test setup and cannot be significantly reduced. Also the temperature of the test specimen holder is monitored, and slight increase of the temperature may be recorded during the course of the tests. This increase can be considered to be too insignificant to have any considerable effect on the test results. Before each test, the pin and disk specimens are cleaned by rinsing them in ethanol, scouring with paper and blowing with pressurized air, and after this they are weighed with a laboratory scale (Precisa Gravimetrics XT 1220M, Precisa Gravimetrics AG) . After the tests, the samples are carefully de- tached from the test machine, and the contact surfaces are observed visually and documented. The wear debris is then carefully removed from the samples by the same procedure as described above. The samples are then weighed again and the mass changes are calculated from the results.

Three specific examples of the powder mixture according to this embodiment of the invention described above are referred to as "mixture A" , "mixture B" and "mixture C" . Mixture A contains 0.5 wt% of silicon carbide, mixture B contains 1.0 wt% of silicon carbide, and mixture C contains 2.0 wt% of silicon carbide. In Fig. 3 FE-SEM images of mixture A (left image) and mixture C (right image) are shown. The steel particles are represented in light colour and the silicon carbide particles appear in dark colour. The images show that the silicon carbide particles are dispersed in the steel powder.

The FE-SEM imaging presented in Fig. 2 and Fig. 3 has been done using the Zeiss ULTRAplus FE-SEM system described above. A small amount of each sample powder has been spread evenly on a piece of electrically conductive carbon tape and mounted to a sample holder. Images have been captured with 10OX magnification using the BSE imaging mode and 15.00 kV acceleration voltage of the electron beam. Three-dimensional objects have been manufactured by the method described above using mixtures A, B, and C as samples for the test methods described above.

For comparison experiments, three-dimensional objects are manu- factured from 316L without reinforcement material using the same method that is used for manufacturing three-dimensional objects using mixtures A, B, and C.

The shapes of the three-dimensional objects are selected such that they are suitable for the respective test method.

In Fig. 4 the measured density and the calculated theoretical density are shown.

The measured density values are very similar to the calculated density values for all of the mixtures A, B, and C. In Fig. 5 the measured tensile and yield strength and their standard deviations are shown.

The increase of the measured tensile strength values has an al- most linear correlation with the concentration of reinforcement material. This means that the selective laser sintering or selective laser melting of a powder mixture of 316L and silicon carbide leads to an effective material strengthening of the manufactured three-dimensional object compared to a three-dimen- sional object manufactured by selective laser sintering or selective laser melting of 316L powder without reinforcement material. Comparably advantageous results have not been obtained using conventional sintering methods. This can be attributed to the rapid heat cycles characteristics of the selective laser sintering or selective melting process and the small amount of retained porosity.

In Fig. 6 the measured hardness together with its standard deviation are shown.

The increase of the measured hardness values has an almost linear correlation with the concentration of reinforcement material. This means that the selective laser sintering or selective laser melting of a powder mixture of 316L and silicon carbide leads to a material hardening of the manufactured three-dimensional object compared to a three-dimensional object manufactured by selective laser sintering or selective laser melting of 316L powder without reinforcement material. In Fig. 7 the pin mass loss and the disk mass loss measured by wear testing are shown. A significantly reduced pin mass in the case of mixtures B and C shows that the selective laser sintering or selective laser melting of a powder mixture of 316L and silicon carbide leads to an increase of the wear resistance of the manufactured three-di- mensional object compared to a three-dimensional object manufactured by selective laser sintering or selective laser melting of 316L powder without reinforcement material.

The increase of the measured disk mass loss values has an almost linear correlation with the concentration of reinforcement material. This means that the selective laser sintering or selective laser melting of a powder mixture of 316L and silicon carbide leads to an increase of the abrasivity of the manufactured three-dimensional object_t compared to a three-dimensional object manufactured by selective laser sintering or selective laser melting of 316L powder without reinforcement material.

The measured values for the rate of uniform corrosion penetration corrosion are 0.0035 mm/yr or lower for the three-dimen- sional objects manufactured as samples by selective laser sintering or selective laser melting of mixture A, mixture B, mixture C, and 316L. They do not show a correlation with the concentration of reinforcement material. This means that it is possible that the corrosion resistance of three-dimensional objects manufactured by selective laser sintering or selective laser melting of a powder mixture of 316L and silicon carbide is not or not significantly reduced compared to a three-dimensional object manufactured by selective laser sintering or selective laser melting of 316L powder without reinforcement material.

In another specific embodiment of the invention, the first material is a 316L grade steel and the second material is titanium carbide (Tic) powder. The powder mixture comprising 316L powder and TiC powder according to this embodiment is used as building material for manufacturing three-dimensional objects by selective laser sintering or selective laser melting using the EOS M100 DMLS-system having a Yb fibre laser as laser sintering or laser melting apparatus 1.

Alternatively, other additive manufacturing techniques such as selective sintering or melting by using an electron beam can be used.

The manufactured three-dimensional objects according to this embodiment consist of a composite material made up of a matrix being at least predominantly a steel matrix with TiC reinforcement particles .

The selection of the process parameters for controlling the additive manufacturing process (for instance spot size of the laser beam or electron beam, beam profile, laser output power, thickness of a powder layer, distance between individual scanning lines of the beam, scanning speed of the beam over the predefined areas to be solidified) follows the principles described above. As described above, a control unit, which may be connected to a database and/or a process monitoring system, can be used therefor.

Furthermore, the parameters and the first and second material can be selected so that proper wetting of reinforcement particles by liquid metal is enabled, resulting in a high material density and a high reinforcement particle adhesion. At the same time, high temperature processing time can be kept short to prevent reinforcement particle dissolution and chemical reactions with the steel used as base metal. The selection of 316L and TiC as first and second materials leads to a reduced dissolution and a reduced reactivity compared to other first and second materials such as 316L and SiC. Low dissolution and reactivity can be advantageous for some applications, whereas high dissolution and reactivity can be advantageous for other applications. Therefore, the selection of the reinforcement material may depend on the degree of dissolution and reactivity which is desired for a given application. It has been found out that the commercial 316L 20um FlexLine default process parameters (as specified in June 2016) provided by EOS GmbH Electro Optical Systems lead to three-dimensional objects having preferred properties, for example preferred mechanical properties. These process parameters have been used for the manufacture of three-dimensional objects in the specific examples of this embodiment.

The reinforcement materials used for the specific examples of this embodiment is a TiC powder product with a median particle size of approximately 30 μτη, with the whole particle size range lying between approximately 0.5 μτη and 100 μτη. TiC powders of this particle size range are, e.g., provided by the companies Sigma-Aldrich and H. C. Starck. The TiC powder contains low amounts of impurities (<0.50 wt% in total) , such as oxygen and free carbon.

The particle size distribution of the TiC powder products has been determinded by means of laser diffraction using a Microtrac S3500 laser diffraction analyzer following standard ISO 13320: 2009-10 "Particle size analysis - Laser diffraction methods". Thereby, the powder particles have been dispersed in a liquid for the analysis. From the selected test parameters, loading factor and transmission values are critical for the accuracy of the method, and these have been set to a loading factor (particle concentration) of 0.0899 and a transmission value of 0.906. Further test parameters are stated below:

Fluid refractive index: 1.333

Power of ultrasonic dispersion: 40 W

Time of ultrasonic dispersion: 300 sec

3 laser system, laser wave length: 780nm

In Fig. 8, a FE-SEM image of the TiC powder as used for the specific examples according to this embodiment is shown. The image shows that the particles of the TiC powder have an angular shape .

In Fig. 9, a FE-SEM image of the 316L powder as used for the specific examples is shown. The image shows that the particles of the 316L powder have a substantially spherical shape. For FE-SEM imaging as presented in Figures 8 and 9, the same technique of sample preparation has been used as in the case of the FE-SEM imaging presented in Fig. 2 and Fig. 3. The image shown in Fig. 8 has been captured with a JEOL JSM 6335F FE-SEM device with 50OX magnification using the SE imaging mode and 20.00 kV acceleration voltage of the electron beam. The image shown in Fig. 9 has been captured with the Zeiss ULTRAplus FE- SEM system described above with 500X magnification using the BSE imaging mode and 15.00 kv acceleration voltage of the electron beam .

The 316L powder is, e.g., obtainable from EOS GmbH Electro Optical Systems under the tradename "EOS StainlessSteel 31SL" . The TiC powder has been mixed with the 316L base metal powder in different concentrations resulting in four specific examples according to this embodiment with 0.75 wt%, 1.5 wt%, 3.0 wt%, and 4 wt% of TiC, respectively.

The powder components have been mixed by dry mechanical mixing using a uniaxial mixer and a mixing process equivalent to the mixing process described above for the embodiment using 316L powder and SiC powder. The mixing has been continued for 20 minutes with 15 rpm rotating speed.

The three-dimensional objects manufactured from the powder mixtures are characterized with respect to various properties . The results are presented below. Results for a three-dimen ional ob- ject manufactured from pure 316L, i.e. an object consisting of unreinforced material, are presented for comparison.

The measured density, the calculated theoretical density and the relative density for the four examples according to this embodi- ment are shown in Fig. 10.

The measured density has been determined by utilizing the Archimedes' principle according to standard ISO 3369. The method is described above.

The theoretical density is calculated based on the theoretical density of solid TiC (4.93 g/cm³) and the measured density of a sample manufactured from 316L without reinforcement material (7.99 g/cm³) . These densities are used for estimating the volume fraction of TiC in the materials. Then, based on these theoretical volume fractions and the stated densities of the solid material constituents, the theoretical densities of the composite materials are calculated. The described procedure can be expressed by the equations

TiC volume fraction = TiC wt% / TiC density / (TiC wt% / TiC density + 316L wt% / 316L density)

316L volume fraction = 316L wt% / 316 L density / (TiC wt% / TiC density + 316L wt% / 316L density) theoretical density of the composite = TiC volume fraction * TiC density + 316L volume fraction * 316L density

The relative density is defined as the ratio of the measured density and the theoretical density.

The selected parameters of the laser sintering or laser melting process and the selected first and second materials have resulted in high relative density values of the manufactured composite material objects. Relative density values of more than 99.0% have been measured for all material compositions.

The structure of the manufactured three-dimensional objects has been found to be free from cracks or other structural defects. TiC particle dissolution has not been detected in these struc- tures . Structural characterization has been performed using optical microscopy, scanning electron microscopy (SEM) and Energy- dispersive X-ray spectroscopy (EDS) .

In Fig. 11, a SEM image showing a TiC particle in the composite structure of a three-dimensional object manufactured from the powder mixture according to the example with a TiC content of 3.0 wt% is shown. The image has been captured with the Zeiss UL- TRAplus FE-SEM system described above an acceleration voltage of 15.0 kV, the SE imaging mode, and 2500X magnification. No particle fracture or reaction phase formation is visible for the TiC particle . Tensile testing has been carried out according to standard ISO 6892-1 : 2009 :B10. The method is described above. Impact testing has been performed according to standard EN ISO 148-1:2010

"Metallic materials - Charpy pendulum impact test - Part 1: Test method" .

Tensile strength and yield strength as well as elongation after fracture and impact energy are shown for the four examples according to this embodiment, in which TiC particles are used, and, for comparison, for a three-dimensional object manufactured from 316L in Fig. 12 and Fig. 13 (The data for tensile strength and yield strength are shown in both Figures) . These results represent the averaged values of three measurements with each material . As a result of TiC particle addition (composite formation) a considerable increase of tensile strength and yield strength of the 316L steel has been found. Also increased wear strength and hardness properties have been measured in this invention in comparison to the unreinforced EOS 316L steel.

A similar increase of tensile strength and yield strength has been found in the case of Sic particle addition and similar reinforcement volume fractions (see mixtures A, B and C

discussed above) .

As is visible from Fig. 12 and Fig. 13, the displayed properties of the composite materials respond rather linearly to the TiC particle concentration. These results can be compared to the results gained with SiC particle reinforcement, see Fig. 5 and the associated description above. The comparison implies that ductility and impact toughness properties of the composites are higher in the case of TiC reinforcement material than in the case of SiC reinforcement material. Relatively low ductility and impact toughness can be advantageous for some applications, whereas relatively high ductility and impact toughness can be advantageous for other applications. Therefore, the selection of the reinforcement material may depend on the degree of ductility and impact toughness which is desired for a given application.

Numerical values of the results obtained for the yield strength, the tensile strength, the elongation after fracture, and the impact energy in the case of Mixtures A, B, and C containing SiC reinforcement material as well as the four examples according to this embodiment using TiC particles are presented in Table 1.

Table 1

Resistance to abrasive wear has been tested by the ball-on-disk -method according to the standard ASTM G99 - 95a. The method is described above. Three-dimensional objects are manufactured as pin specimens by selective laser sintering or selective laser melting. No additional surface treatment is done. The following parameters have been chosen for the tests: Normal force = 40.0 N, sliding speed = 0.25 m/s, sliding distance = 450.0 m, test time = 30.0 min.

Results for the four examples according to this embodiment, in which TiC particles are used, are presented in Fig. 14. The results are expressed as the mass loss of the composite pin samples during testing. Smaller mass loss indicates better wear resistance. The bar labelled with "Ref" represents the pin mass loss of a specimen manufactured from 316L material without reinforcement material. The numerical values of the reults obtained for the pin mass loss in the case of the Mixtures A, B, and C containing SiC reinforcement material as well the four examples according to this embodiment using TiC particles are presented in Table 2. The labelling "1.2 vol% reinforced samples" stands for Mixture A and the mixtures of 316L and 0.75 wt% TiC. The labelling "2.5 vol% reinforced samples" stands for Mixture B and the mixtures of 316L and 1.75 wt% TiC. The labelling "4.8 vol% reinforced samples" stands for Mixture C and the mixtures of 316L and 3.0 wt% TiC.

Table 2

1.2 vol% 2.5 vol% 4.8 vol%

Material reinforced reinforced reinforced samples samples samples

316L reference (no

0.026 g 0.026 g 0.026 g reinforcement material)

SiC 0.024 g 0.011 g 0.007 g

TiC 0.020 g 0.018 g 0.012 g Wear resistance of the 316L steel is also significantly increased by the TiC particle addition.

In the case of this embodiment, hardness testing has been done at EOS Finland Oy with Struers Duravision 20 hardness testing machine. The test procedures follows the standards ISO 6507- 1:2005 "Metallic materials — Vickers hardness test —Part 1: Test method" and ISO 6508-1:2015 "Metallic materials - Rockwell hardness test — Part 1: Test method". The hardness has been measured by Rockwell and Vickers methods. The results are presented in HRC and HV10 hardness units and the values are reported with the accuracy of 0.1 HRC and 1 HV10 respectively. The hardness has been measured 5 times for each sample using both methods . The test samples have been ground with Struers LaboPol-5 grinding and polishing machine using Struers SiC #80 and #320 abrasive papers before testing.

In the Rockwell method using the C scale diamond cone, the in- denter is forced into the tested material. First a specified preliminary force is applied and the initial indentation depth is measured. After this an additional force is applied and removed, and the final indentation depth is measured. The Rockwell hardness value is then derived from the following equation:

Rockwell Hardness = XJT ^h ,

s

Where h is the difference between the final and initial

indentation depths and N and s are constants . The standard states that only values between 20 and 70 HRC are applicable for this method and in this study some samples were softer than 20

HRC. This is not considered a problem since the hardness has also been measured by Vickers method and the results have been used used to indicate a trend rather than to compare exact values .

In the Vickers method a pyramid shaped diamond indenter with a 136° angle between opposite faces is forced into the surface of the sample and the diagonal length of the indentation in the surface is measured after removing the test force. In HV10 the used test force is 98,07N. Hardness Vickers value can be

determined from the following formula

136°

0,102(2Fsin

HV = ^ d^{2 2} 0,189F

where F is the test force and d is the average of the two diagonal lengths . Results are shown in Fig. 15 for the four examples according to this embodiment. The results have been obtained by calculating the average values from 5 measurements with each sample and test method. Numerical values of the results obtained for the hardness in the case of Mixtures A, B, and C containing SiC reinforcement material as well as the four examples according to this

embodiment using TiC particles are presented in Table 3. Table 3

HV10 HRC

Material

(average) (average)

316L ref 202 12.826

Mixture A: 0.5 wt% SiC 238 26.184

Mixture B: 1.0 wt% SiC 256.6 29.4975

Mixture C: 2.0 wt% SiC 353.6 37.174

0.75wt% TiC 233 19.372

1.5wt% TiC 244.4 22.654

3.0wt% TiC 282.6 29.1075 Hardness of the 316L steel is also significantly increased by the Tie particle addition. The corrosion resistance for composite materials made by laser sintering or laser melting of the powder mixtures comprising Tic according to this embodiment using Tie particles has been analyzed by salt water immersion for 30 days according to standards NACE TM0169/G31 - 12a "Standard Guide for Laboratory Immersion Corrosion Testing of Metals". The method is described above. No visible or measurable corrosion was seen on any of the samples according to this embodiment after the 30 days immersion in salt water, the measured mass change after 30 days salt water immersion was 0,000g with all samples with samples grinded with P320 SiC paper.

In another specific embodiment of the invention, the first material is a 316L grade steel and the second material is tungsten carbide (WC) powder.

The powder mixture comprising 316L powder and WC powder according to this embodiment is used as building material for manufacturing three-dimensional objects by selective laser sintering or selective laser melting using the EOS M100 DMLS-system having a Yb fibre laser as laser sintering or laser melting apparatus 1.

Alternatively, other additive manufacturing techniques such as selective sintering or melting by using an electron beam can be used. The manufactured three-dimensional objects according to this embodiment consist of a composite material made up of a matrix being at least predominantly a steel matrix with WC reinforcement particles .

The selection of the process parameters for controlling the additive manufacturing process (for instance spot size of the laser beam or electron beam, beam profile, laser output power, thickness of a powder layer, distance between individual scan- ning lines of the beam, scanning speed of the beam over the predefined areas to be solidified) follows the principles described above. As described above, a control unit, which may be connected to a database and/or a process monitoring system, can be used therefor.

Furthermore, the parameters and/or the first and/or second material have been selected so that wetting of reinforcement particles by liquid metal is sufficient, resulting in a high material density and a high reinforcement particle adhesion. At the same time, high temperature processing time may be kept short to prevent reinforcement particle dissolution and chemical reactions with the steel used as base metal. The selection of 316L and WC as first and second materials may lead to a reduced dissolution and a reduced reactivity compared to other first and second ma- terials such as 316L and SiC. Low dissolution and reactivity can be advantageous for some applications, whereas high dissolution and reactivity can be advantageous for other applications.

Therefore, the selection of the reinforcement material depends on the degree of dissolution and reactivity which is desired for a given application.

It has been found out that the commercial 316L 20um FlexLine default process parameters (as specified in June 2016) provided by EOS GmbH Electro Optical Systems lead to three-dimensional objects having preferred properties, for example preferred mechanical properties. These process parameters have been used for the manufacture of three-dimensional objects in the specific exam- pies of this embodiment .

The reinforcement material used for the specific examples of this embodiment is a WC powder product with a median particle size of approximately 25 μΐΏ, with the whole particle size range lying between approximately 5 μτη and 125 μτη. WC powder of this particle size range is, e.g., provided by the company H. C.

Starck.

The particle size distribution of the WC powder product has been determined by means of laser diffraction using a Microtrac S3500 laser diffraction analyzer following standard ISO 13320: 2009-10 "Particle size analysis - Laser diffraction methods" . Thereby, the powder particles have been dispersed in a liquid for the analysis. From the selected test parameters, loading factor and transmission values are critical for the accuracy of the method, and these have been set to a loading factor (particle concentration) of 0.0573 and a transmission value of 0.948.

Further test parameters are stated below:

Fluid refractive index: 1.333

Power of ultrasonic dispersion: 40 W

Time of ultrasonic dispersion: 300 sec

3 laser system, laser wave length: 780nm The WC powder may contain low amounts of impurities (preferably

<0.10 wt% in total), such as oxygen and free carbon. In Fig. 16, a FE-SEM image of the WC powder as used for the specific examples according to this embodiment is shown. The image shows that the particles of the WC powder have a spherical shape. For FE-SEM imaging, the same technique of sample preparation has been used as in the case of the FE-SEM imaging presented in Figures 2 and 3. The image shown in Fig. 16 has been captured with a Hitachi S-3500N FE-SEM device with 500X magnification using the SE imaging mode and 20.00 kV acceleration volt- age of the electron beam.

A FE-SEM image of the 316L powder as used for the specific examples is shown in Fig. 9. The 316L powder is, e.g., obtainable from EOS GmbH Electro Optical Systems under the tradename "EOS StainlessSteel 316L" .

The WC powder has been mixed with the 316L base metal powder in different concentrations resulting in four specific examples ac- cording to this embodiment with 2.5 wt%, 5.0 wt%, 7.5 wt%, and

10.0 wt% of WC, respectively.

The powder components have been mixed by dry mechanical mixing using a uniaxial mixer and a mixing process equivalent to the mixing process described above for the embodiments using 316L powder and SiC or TiC powder. The mixing has been continued for 20 minutes with 15 rpm rotating speed.

The three-dimensional objects manufactured from the powder mix- tures are characterized with respect to various properties. The results are presented below. Results for a three-dimensional object manufactured from pure 316L, i.e. an object consisting of unreinforced material, are presented for comparison. The measured density, the calculated theoretical density and the relative density for the four examples according to this embodiment are shown in Fig. 17.

The measured density has been determined by utilizing the Archimedes' principle according to standard ISO 3369. The method is described above . The theoretical density is calculated based on the theoretical density of solid WC (15.63 g/cm³)and the measured density of a sample manufactured from 316L without reinforcement material (7.99 g/cm³) . These densities are used for estimating the volume fraction of WC in the materials. Then, based on these theoreti- cal volume fractions and the stated densities of the solid material constituents, the theoretical densities of the composite materials are calculated. The described procedure can be expressed by the equations WC volume fraction = WC wt% / WC density / (WC wt% / WC density + 316L wt% / 316L density)

316L volume fraction = 316L wt% / 316 L density / (WC wt% / WC density + 316L wt% / 316L density) theoretical density of the composite = WC volume fraction * WC density + 316L volume fraction * 316L density

The selected parameters of the laser sintering or laser melting process and the selected first and second materials have resulted in high relative density values of the manufactured composite material objects. That the calculated relative density values are slightly higher that 100% may be explained by the assumption that the volume of the steel material and the WC material is not strictly additive in the four examples in contrast to the assumption underlying the calculation of the theoretical density.

The structure of the manufactured three-dimensional objects has been found to be free from cracks or other structural defects indicating that the properties of the interface between the metal and the WC particles are favourable. WC particle dissolution has not been detected in these structures. Structural characterization has been performed using optical microscopy and scanning electron microscopy (SEM) . In Fig. 18, a SEM image showing a WC particle in the composite structure of a three-dimensional object manufactured from the powder mixture according to the example with a WC content of 5.0 wt% is shown. The image has been captured with a Hitachi S-3500N SEM-system with SE- and BSE-detectors , using the SE-mode, 2500X magnification and 15,0kV acceleration voltage. No particle fracture or reaction phase formation is visible for the WC particle.

Tensile testing has been carried out according to standard ISO 6892-1 : 2009 : B10. The method is described above. Impact testing has been performed according to standard EN ISO 148-1:2010.

Tensile strength and yield strength as well as elongation after fracture are shown for the four examples according to this embodiment, in which WC particles are used, and, for comparison, for a three-dimensional object manufactured from 316L in Fig. 19. These results represent the averaged values of three

measurements with each material. As a result of WC particle addition (composite formation) a considerable increase of tensile strength and yield strength of the 316L steel has been found. Also increased wear strength and hardness properties have been measured in this invention in comparison to the unreinforced EOS 316L steel.

As is visible from Fig. 19, the displayed properties of the composite materials respond rather linearly to the WC particle concentration. These results can be compared to the results gained with SiC particle reinforcement and WC particle

reinforcement, see Figures 5, 12, and 13 and the associated description above. The comparison implies that ductility and strength properties of the composites are higher in the case of WC reinforcement material than in the case of SiC reinforcement material, and comparable to the properties of TiC reinforcement material. It should be noted that due to the different inherent density properties of WC, SiC and TiC particles, similar

concentrations of these particles expressed in wt% do not correspond to their similar concentrations in vol-%. Relatively low ductility and impact toughness can be advantageous for some applications, whereas relatively high ductility and impact toughness can be advantageous for other applications. Therefore, the selection of the reinforcement material may depend on the degree of ductility and impact toughness which is desired for a given application.

Numerical values of the results obtained for the yield strength, the tensile strength, the elongation after fracture, and the impact energy for the four examples according to this embodiment using WC particles are presented in Table 4.

Table 4 Rp 0.2 Rm A

[MPa] [MPa] [%] [J]

Material Elongation

Yield Tensile Impact after

strength strength energy fracture

316L 589.6 679.0 36.9 18.3

2.5 wt% WC 709.8 786.2 26.9 12.7

5.0 wt% WC 844.6 967.8 20.8 8.0

7.5 wt% WC 914.6 1056.2 11.1 3.7

10.0 wt% WC 1094.6 1264.5 7.1 2.7

Results of the examples according to this embodiment, in which 5.0 wt% and 10 wt% WC particles are used, are presented in Fig. 20. The results represent the averaged values of three test repetitions with each material. The results are expressed as the mass loss of the composite pin samples during testing. Smaller mass loss indicates better wear resistance. The bar labelled with "Ref " represents the pin mass loss of a specimen

manufactured from 316L material without reinforcement material.

Wear resistance of the 316L steel is also significantly increased by the WC particle addition.

In the case of this embodiment using WC particles, hardness testing has been done at EOS Finland Oy with Struers Duravision 20 hardness testing machine. The test procedure follows the standards ISO 6507-1:2005 "Metallic materials — Vickers hardness test -Part 1: Test method" and ISO 6508-1:2015 "Metallic

materials — Rockwell hardness test — Part 1: Test method".

Further details about the Rockwell method are described above. The hardness has been measured by Rockwell and Vickers methods. The results are presented in HRC and HV10 hardness units. The hardness has been measured 5 times for each sample using both methods. The test samples have been ground with Struers LaboPol-5 grinding and polishing machine using Struers SiC #80 and #320 abrasive papers before testing.

Results are shown in Fig. 21 for the four examples according this embodiment using WC particles. The results have been obtained by calculating the average values from 5 measurements with each sample and test method. Numerical values of the results are presented in Table 5.

Table 5

As can be seen from the results, hardness of the 316L steel is also significantly increased by the WC particle addition.

The corrosion resistance for composite materials made by laser sintering or laser melting of the powder mixtures comprising WC according to this embodiment has been analyzed by salt water immersion for 30 days according to the standard NACE TM0169/G31 - 12a "Standard Guide for Laboratory Immersion Corrosion Testing of Metals" The method is described above. No visible or measurable corrosion was seen on any of the samples according to this embodiment after the 30 days immersion in salt water, the measured mass change after 30 days salt water immersion was 0,000g with all samples with samples grinded with P320 SiC paper.

According to the present invention, it is possible to select an appropriate first material and an appropriate second material depending on the desired properties of the manufactured three- dimensional objects. For instance, tensile strength as well as yield strength of 316L can be increased by addition of SiC, TiC, or WC. The effect on the ductility is different for these reinforcement materials. Depending on whether a high ductility is desired or not, WC, TiC, SiC or mixtures thereof can be chosen as reinforcement material for 316L.

While the present invention has been described by means of selective laser sintering or selective laser melting, respectively, the present invention is not limited to selective laser sintering or selective laser melting. The present invention may be applied to any possible methods for producing a three-dimensional object by applying in layers and selectively solidifying a building material in powder form by means of electromagnetic and/or particle radiation. The irradiation device may contain one or more lasers. The lasers may be gas lasers, solid-state lasers or lasers of any other kind, e.g. laser diodes, especially arrays having VCSEL (Vertical Cavity Surface Emitting Laser) or VECSEL (Vertical External Cavity Surface Emitting Laser) , or any combination thereof. In general, any irradiation device by means of which energy may be selectively applied onto a layer of the building material and suitable for solidifying the building material may be used. This may be a light source different from a laser, an electron beam, or any other suitable energy source or radiation source. The invention may also be applied to selective mask sintering, in which a mask and an expanded light source are used instead of a deflected laser beam, or to absorption sintering or inhibition sintering.

Claims

1. Powder mixture for use in the manufacture of a three-dimen- sional object by means of an additive manufacturing method,

wherein the powder mixture comprises a first material and a second material,

wherein the first material comprises a steel in powder form,

wherein the second material comprises a reinforcement material different from the first material, and

wherein the powder mixture is adapted to form a composite object when solidified by means of an electromagnetic and/or a particle radiation in the additive manufacturing method.

2. Powder mixture according to claim 1,

wherein the reinforcement material is embedded in a matrix of the composite object at least partially in a chemically unmodified form.

3. Powder mixture according to any of the preceding claims, wherein the steel contains Fe and

max 0.10 wt% C,

2.00 - 3.00 wt% Mo,

10.00 - 15.00 wt% Ni, and

16.00 - 19.00 wt% Cr,

wherein preferably the steel further contains

max 0.030 wt% S,

max 0.045 wt% P,

max 0.16 wt% N,

max 0.50 wt% Cu,

max 1.00 wt% Si, and

max 2.00 wt% Mn.

4. Powder mixture according to any one of the preceding claims ,

wherein the median grain size of the first material is 1 μηη or more, preferably 5 pm or more, more preferably 10 m or more, and/or 150 μπα or less, preferably 75 μιη or less.

5. Powder mixture according to any one of the preceding claims ,

wherein the particles of the first material are substantially spherical.

6. Powder mixture according to any one of the preceding claims ,

wherein the reinforcement material comprises at least one non-metallic material,

wherein preferably the non-metallic material is one out of borides and carbides and nitrides and oxides and silicides and graphite .

7. Powder mixture according to claim 6,

wherein more preferably the reinforcement material comprises silicon carbide,

wherein most preferably the reinforcement material is sili- con carbide.

8. Powder mixture according to claim 6,

wherein the reinforcement material comprises titanium carbide ,

wherein preferably the reinforcement material is titanium carbide .

9. Powder mixture according to claim 6, wherein the reinforcement material comprises tungsten carbide ,

wherein preferably the reinforcement material is tungsten carbide .

10. Powder mixture according to any one of the preceding claims ,

wherein the reinforcement material is a powder,

wherein the median grain size of the reinforcement material is 0.5 μτη or more, preferably 1 μηη or more, and/or 100 μτη or less, preferably 50 μτη or less.

11. Powder mixture according to any one of the preceding claims ,

wherein the particles of the reinforcement material have a substantially spherical or a substantially angular or a substantially irregular shape.

12. Powder mixture according to any one of the preceding claims,

wherein the content of the reinforcement material is

0.05 wt% or more, preferably 0.1 wt% or more, more preferably 0.3 wt% or more, still more preferably 0.5 wt% or more, and/or wherein the content of the reinforcement material is 40 wt% or less, more preferably 10 wt% or less, still more preferably 5 wt% or less,

13. Method for the production of a powder mixture according to any one of the preceding claims,

wherein the powder mixture is produced by mixing the first material and the second material in a predetermined mixing ratio, and

wherein preferably the mixing is a dry mixing.

14. Method for the manufacture of a three-dimensional object from a powder mixture according to any of claims 1 to 12 by selective layer-wise solidification of the powder mixture by means of an electromagnetic radiation and/or a particle radiation at positions that correspond to a cross-section of the object in a respective layer.

15. Method according to claim 14, comprising the steps:

solidifying the powder mixture selectively at positions corresponding to a cross-section of the three-dimensional object in the layer, and

repeating the steps of applying and solidifying until the three-dimen ional object is completed.

16. Three-dimensional object manufactured from a powder mixture according to any of claims 1 to 12 by selective layer-wise so- lidification of the powder mixture by means of an electromagnetic radiation and/or particle radiation at positions that correspond to a cross-section of the object in a respective layer.

17. Three-dimensional object according to claim 16,

wherein the reinforcement material is embedded in a matrix of the three-dimensional object at least partially in a chemically unmodified form.

18. Three-dimensional object according to any of claims 16 or 17,

wherein the material of the three-dimensional object has a tensile strength of 500 MPa or more, preferably 800 MPa or more, more preferably 900 MPa or more, and/or wherein the material of the three-dimensional object has a yield strength of 170 MPa or more, preferably 400 MPa or more, more preferably 600 MPa or more.

19. Three-dimensional object according to any of claims 16 to 18,

wherein a reduction of a pin mass loss in wear testing of the three-dimensional object compared to a pin mass loss in wear testing of a three-dimensional object manufactured from the first material by selective layer-wise solidification of the first material by means of the electromagnetic and/or particle radiation at positions that correspond to a cross -section of the object in a respective layer is 25% or more, preferably 50% or more, more preferably 75% or more, and/or

wherein an increase of a disk mass loss in wear testing of the three-dimensional object compared to a disk mass loss in wear testing of a three-dimensional object manufactured from the first material by selective layer-wise solidification of the first material by means of the electromagnetic and/or particle radiation at positions that correspond to a cross-section of the object in a respective layer is 15% or more, preferably 50% or more, more preferably 70% or more.

20. Control unit for an apparatus for manufacturing a three-di- mensional object layer by layer by applying and selectively solidifying a powder mixture according to any of claims 1 to 12 by means of an electromagnetic and/or particle radiation,

wherein the control unit is adapted to control that a predefined amount of energy is introduced into a defined volume of the powder mixture by means of the electromagnetic and/or particle radiation, and

wherein preferably an upper limit of the predefined amount of energy is selected such that the reinforcement material is not completely dissolved during the time in which the predefined amount of energy is applied to the defined volume of the powder mixture ,

wherein the upper limit of the predefined amount of energy is preferably defined such that the reinforcement material of the powder mixture is dissolved to 70 wt% or less, preferably 50 wt% or less, more preferably 30 wt% or less, even more preferably 5 wt% or less during the time in which the predefined amount of energy is applied to the defined volume of the powder mix- ture .

21. Method for the manufacture of a three-dimensional object from a powder mixture by selective layer-wise solidification of the powder mixture by means of an electromagnetic and/or a par- ticle radiation at positions that correspond to a cross-section of the object in a respective layer,

wherein the powder mixture comprises a first material and a second material,

wherein the first material comprises a metal in powder form,

wherein the second material comprises a reinforcement material ,

wherein the powder mixture is selectively solidified by means of an electromagnetic and/or a particle radiation at posi- tions that correspond to a cross-section of the object in a respective layer forming a composite material, and

wherein 90 wt% or less, preferably 70% or less, more preferably 50% or less, still more preferably 30% or less, even more preferably 5 wt% or less of the reinforcement material are dis- solved in the metal.