[go: up one dir, main page]

WO2016013496A1 - Structure d'alliage et procédé de production de structure d'alliage. - Google Patents

Structure d'alliage et procédé de production de structure d'alliage. Download PDF

Info

Publication number
WO2016013496A1
WO2016013496A1 PCT/JP2015/070470 JP2015070470W WO2016013496A1 WO 2016013496 A1 WO2016013496 A1 WO 2016013496A1 JP 2015070470 W JP2015070470 W JP 2015070470W WO 2016013496 A1 WO2016013496 A1 WO 2016013496A1
Authority
WO
WIPO (PCT)
Prior art keywords
alloy
concentration
less
solidified
powder
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/JP2015/070470
Other languages
English (en)
Japanese (ja)
Inventor
孝介 桑原
隆彦 加藤
青田　欣也
高橋　勇
正 藤枝
山賀　賢史
佐竹　弘之
元 村上
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Hitachi Ltd
Original Assignee
Hitachi Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Priority claimed from JP2014150020A external-priority patent/JP6459272B2/ja
Priority claimed from JP2014151331A external-priority patent/JP6443721B2/ja
Application filed by Hitachi Ltd filed Critical Hitachi Ltd
Publication of WO2016013496A1 publication Critical patent/WO2016013496A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

Links

Images

Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/10—Sintering only
    • B22F3/105—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/12—Both compacting and sintering
    • B22F3/16—Both compacting and sintering in successive or repeated steps
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y10/00—Processes of additive manufacturing
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y80/00—Products made by additive manufacturing

Definitions

  • the present invention relates to an alloy structure and a method of manufacturing the alloy structure.
  • Alloy materials are used in a variety of applications including structural members that form the framework of structures and devices, various mechanical members, etc. For applications in harsh environments where it is difficult to use steel or aluminum materials It is often used.
  • nickel-based alloys, cobalt-based alloys and the like have been developed which are applied to turbine members and the like provided in aircraft, generators and the like and can be applied to ultra-high heat environments of 1000 ° C. or more.
  • high alloy steels and the like that can exhibit high corrosion resistance and wear resistance even under such ultra-high heat environment are also developed.
  • high-entropy alloys As a type of alloy material A multi-element alloy called is attracting attention.
  • a high entropy alloy is considered to be an alloy which is composed of about five or more kinds of plural elements and which contains each element at an equal atomic ratio or an atomic ratio in the vicinity thereof. Since it has the feature that the rate of atomic diffusion is slow and is excellent in heat resistance, high temperature strength, corrosion resistance and the like, application to applications in severe environments is expected.
  • Patent Document 1 discloses a method for producing a cemented carbide composite material, in which at least one ceramic phase powder and a multicomponent high entropy alloy powder are mixed to form a mixture The steps of: compacting the mixture; and sintering the mixture to form a cemented carbide composite, wherein the multicomponent high entropy alloy powder comprises 5 to 11 major elements, each major element There is disclosed a manufacturing method in which 5% to 35% by mole of the multicomponent high entropy alloy powder is contained.
  • Non-Patent Document 1 discloses that in a high entropy alloy having an equiatomic ratio of Al, Co, Cr, Fe, and Ni, analysis of the dimensional effect on the microstructure and mechanical properties is disclosed.
  • the main elements constituting the high-entropy alloy are dissolved in an equiatomic ratio
  • the alloy material disclosed in Non-Patent Document 1 is only a small piece of 10 mm in diameter ⁇ 70 mm in height (volume 5495 mm 3 ) even for the largest prototype material, and it is difficult to apply as a material of a structure.
  • an object of the present invention is to provide an alloy structure having an arbitrary shape and size with high uniformity of distribution of elemental composition and mechanical strength, and having good high temperature strength and corrosion resistance.
  • the present invention adopts, for example, the configuration described in the claims.
  • FIG. 1 It is a conceptual diagram which shows an example of the process of the manufacturing method of the alloy material which concerns on this embodiment. It is sectional drawing which showed the outline of the metal structure which an alloy structure has.
  • (A) is a cross-sectional view of the alloy structure according to the present embodiment
  • (b) is an enlarged cross-sectional view of part A in (a)
  • (c) is a schematic view of the metal structure of the alloy material according to the comparative example. It is sectional drawing which showed.
  • FIG. 7 is a view showing the shape and dimensions of an alloy structure according to Example 3;
  • FIG. 16 is a compression true stress-compression true strain diagram in the alloy structure according to Example 3.
  • FIG. 18 is a view showing test temperature dependency of tensile strength in the alloy structure according to Example 4.
  • the alloy structure according to the present embodiment includes aluminum (Al), cobalt (Co), chromium ( Cr), high-entropy alloys based on iron (Fe) and nickel (Ni), It is a metal shaped article formed into a desired shape and dimension by additive manufacturing.
  • This alloy structure contains the elements of Al, Co, Cr, Fe and Ni at an atomic concentration in the range of 5 at% or more and 30 at% or less for each element, and at least four of these elements are contained.
  • the atoms of Al, Co, Cr, Fe and Ni form a solid solution phase in which these five elements are solidly dissolved.
  • this alloy structure has high heat resistance, high temperature strength, wear resistance, and corrosion resistance as general properties as a high entropy alloy.
  • this alloy structure has a unique solidified structure formed by additive manufacturing, and has a feature of high uniformity of distribution of elemental composition and mechanical strength.
  • the main crystals substantially consist of a collection of columnar crystals at normal temperature and normal pressure.
  • the presence ratio of columnar crystals is at least 50% or more in an occupied area ratio in any cross section of the solidified structure, and is 90% or more or 95% or more according to the formation condition of the solidified structure in the manufacturing method described later It is also possible.
  • the average crystal grain size of the columnar crystals is 100 ⁇ m or less, and it is also possible to further refine it to 10 ⁇ m or less.
  • the average grain size can be determined according to the method defined in JIS G 0551 (2013).
  • the main crystals of the alloy material structure have a crystal structure of face-centered cubic lattice or body-centered cubic lattice at normal temperature and normal pressure.
  • the composition By selectively designing the composition, it is possible to make the existing ratio of the crystal structure of the face-centered cubic lattice 90% or more or 95% or more in the occupied area ratio in any cross section of the solidified structure.
  • the proportion of the crystal structure of the body-centered cubic lattice can be 90% or more or 95% or more in an occupied area ratio in an arbitrary cross section of the solidified structure.
  • the alloy structure can have an elemental composition containing Al, Co, Cr, Fe and Ni, as well as other additive elements.
  • additive elements for example, Si, P, Ti, V, Mn, Cu, Zn, Ga, Ge, As, Se, Nb, Mo, Tc, Ru, Rh, Pd, Ag, Sn, Sb, Te , Ta, W, Re, Os, Ir, Pt, Au and the like.
  • the additive element is added in an atomic concentration range in which the atomic concentration is 10 at% or less, and in the atomic concentration range, one kind of element may be added or plural kinds of elements may be added. However, when adding Ti, the atomic concentration per alloy structure is made less than 5 at%.
  • the alloy structure is allowed to contain elements of Al, Co, Cr, Fe and Ni and additive elements, as well as other unavoidable impurities.
  • an element of unavoidable impurities for example, P , Si, S, Sn, Sb, As, Mn, O, N and the like.
  • P is preferably 0.005 wt% or less, more preferably 0.002 wt% or less
  • Si is preferably 0.040 wt% or less, more preferably 0.010 wt% or less
  • S is Preferably, the content is 0.002 wt% or less, more preferably 0.001 wt% or less, for Sn preferably 0.005 wt% or less, more preferably 0.002 wt% or less, for Sb preferably 0.002 wt% Or less, more preferably 0.001 wt.
  • the content of As is preferably 0.005 wt% or less, more preferably 0.001 wt% or less, and the content of Mn is preferably 0.050 wt% or less, more preferably 0 . Limit to 020 wt% or less.
  • O is preferably 0.001 wt% or less (10 ppm or less), more preferably 0.0003 wt% or less (3 ppm or less), and N is preferably 0.002 wt% or less (20 ppm or less), more preferably Is 0.0 Limit to 01 wt% or less (10 ppm or less).
  • the concentration of unavoidable impurities contained in the alloy structure by limiting the concentration of unavoidable impurities contained in the alloy structure, the uniformity of the distribution of the elemental composition and the mechanical strength can be further enhanced regardless of the shape and size of the structure.
  • the alloy structure contains an element of P, Si, Sn, Sb, As, or Mn as an additive element, the concentration of the element does not have to be limited in this manner.
  • the alloy structure contains at least four elements of Al, Co, Cr, Fe and Ni in a substantially equiatomic ratio in the range of an atomic concentration of 15 at% or more and 23.75 at% or less.
  • the other one element is contained in the atomic concentration range of 5 at% or more and 30 at% or less, and the balance is configured by at least one of the additive element and the unavoidable impurity at 10 at% or less.
  • substantially equal atomic ratio means that the difference in atomic concentration is in the range of less than 3 at%.
  • the element type and atomic ratio that constitute the alloy structure can be selected and designed by, for example, determining the enthalpy of formation, the entropy or the Gibbs energy by thermodynamic calculation.
  • the ratio of the atomic concentrations of four elements contained in equal atomic proportions to one other element is the range of the atomic concentration described above Can be changed as appropriate.
  • the crystal structure of the alloy structure can be changed by changing the ratio of the atomic concentrations of these main component elements, and the mechanical strength, the spreadability, the hardness, the density, and the like can be adjusted.
  • a first principle calculation method a Calphad (Calculation of phase diagrams) method, a molecular dynamics method, a phase-field method, a finite element method or the like can be used in combination as appropriate.
  • the alloy structure contains, for example, Al in an atomic concentration range of 5 at% or more and 30 at% or less, and substantially in an atomic concentration range of 15 at% or more and 23.75 at% or less of Co, Cr, Fe and Ni. It can be set as the elemental composition contained by an equiatomic ratio.
  • the atomic concentration of Al contained in the alloy structure is reduced in the range of 5 at% or more and 30 at% or less, the main phase of the alloy structure can be made to have a crystal structure of face-centered cubic lattice.
  • the main phase of the alloy structure can be made to have a crystal structure of a body-centered cubic lattice.
  • the atomic concentration of Al contained in the alloy structure is 5 at% or more, there is a low possibility that the mechanical strength of the alloy structure is excessively reduced, and on the other hand, the atomic concentration of Al contained in the alloy structure is 30 at. If the content is less than 10%, the main phase of the alloy structure does not easily become an Al-based intermetallic compound, and therefore, the possibility of the ductility of the alloy material being excessively reduced is low.
  • Co is contained substantially at an atomic ratio of 5 at% to 30 at%
  • Al, Co, Fe and Ni are contained in an equiatomic ratio substantially in an atomic concentration range of 15 at% or more and 23.75 at% or less, or 5 at% or more and 30 at% or less of Fe, Al, Co , Cr and Ni in an atomic ratio range of 15 at% or more and 23.75 at% or less substantially, or at least 5 at% or more and 30 at% or less of Ni, and 15 at% or more of Al, Co, Cr, and Fe It is also possible to contain substantially equiatomic proportions in the atomic concentration range of 23.75 at% or less.
  • the alloy structure according to the present embodiment can be manufactured by powder laminate molding using an alloy powder.
  • the method for producing an alloy structure according to the present embodiment includes a powder preparation step of preparing an alloy powder used for layered formation, and a lamination forming step of shaping an alloy structure using the prepared alloy powder.
  • an alloy powder is prepared which contains the same main component and additive elements as the alloy structure to be produced, and has an elemental composition in which the main components are substantially equiatomic.
  • the alloy powder is preferably in the form of a particle assembly in which each powder particle has substantially the same elemental composition as the alloy structure to be produced.
  • a part of the alloy components may be volatilized and lost, so the range of the atomic concentration is set to a high range in consideration of the composition change due to such volatilization. It is also good.
  • a method of producing a metal powder which is conventionally and generally used can be used.
  • an atomizing method in which a molten metal alloy is sprayed with a fluid to be scattered and solidified
  • a crushing method in which a molten metal alloy is solidified and then mechanically crushed, a metal alloy is mixed, and pressure welding and crushing are repeated to form an alloy
  • An appropriate method such as an ingot method, a melt spinning method in which a molten alloy of alloy is caused to flow down on a rotating roll to solidify can be used.
  • the atomizing method is suitable, and the gas atomizing method is more preferably used, and the gas atomizing method performed in an inert gas atmosphere using an inert gas as a fluid is more preferably used.
  • the gas atomizing method it is possible to prepare an alloy powder having high sphericity and less contamination with impurities.
  • the resistance at the time of spreading the alloy powder in lamination molding can be suppressed, so that unevenness of the alloy powder can be reduced.
  • an inert gas the mixing of oxide impurities and the like is suppressed, so that the metal structure of the manufactured alloy material can be made more uniform.
  • the alloy powder can have an appropriate particle diameter according to the melting conditions such as the method of spreading the alloy powder in lamination molding and the output of a heat source for melting the alloy powder.
  • the particle size distribution of the alloy powder is preferably in the range of 1 ⁇ m to 500 ⁇ m. If the particle size of the alloy powder is 1 ⁇ m or more, rolling up and floating of the alloy powder are suppressed, or the oxidation reactivity of the metal is suppressed, thereby reducing the possibility of dust explosion and the like. On the other hand, if the particle diameter of the alloy powder is 500 ⁇ m or less, it is advantageous in that the surface of the solidified layer formed in lamination molding tends to be smooth.
  • FIG. 1 is a conceptual diagram which shows an example of the process of the manufacturing method of the alloy structure which concerns on this embodiment.
  • the layered manufacturing process shown in order from FIG. 1 (a) to (g) is repeatedly performed to perform three-dimensional formation of the alloy structure.
  • the lamination molding process can be carried out using a powder lamination molding apparatus for metal generally used conventionally, and the alloy powder prepared in the powder preparation process is a raw material of such lamination molding process. It is used as a powder.
  • a heating means provided in the layered modeling apparatus for example, one based on an appropriate heating principle such as electron beam heating, laser heating, microwave heating, plasma heating, condensing heating, high frequency heating and the like is used.
  • a lamination molding apparatus by electron beam heating or laser heating is particularly preferable. Electron beam heating or laser heating is relatively easy to control the output of the heat source, the miniaturization of the heated region of the alloy powder, the shaping accuracy of the alloy structure, and the like.
  • the layer forming process includes a powder spreading process and a solidified layer forming process.
  • a layered solidified structure (coagulated layer) is formed through steps shown in FIG. 1A to FIG. 1G sequentially, and formation of the layered solidified structure (coagulated layer) is repeated. , Forming an alloy structure consisting of a set of solidified structures.
  • the layered manufacturing apparatus is provided with a vertically movable piston having a base mounting table 21 at its upper end.
  • a processing table 22 which is not interlocked with the piston is provided around the substrate mounting table 21, and a powder feeder (not shown) for supplying the raw material powder 10 onto the processing table 22 spreads the supplied raw material powder 10.
  • the recoater 23, the heating means 24 for heating the raw material powder 10, an air blast (not shown) for removing the raw material powder 10 on the processing table 22, a temperature controller (not shown) and the like are provided.
  • the processing table 22 and these devices are accommodated in a chamber, and the atmosphere in the chamber is a vacuum atmosphere or an inert gas atmosphere such as argon gas according to the type of the heating means 24 and the atmosphere pressure and temperature are It is supposed to be managed.
  • the base material 15 is previously mounted on the base material mounting table 21 and aligned so that the surface to be molded (upper surface) of the base material 15 and the upper surface of the processing table 22 are flush with each other .
  • the base material 15 Any appropriate material can be used as the base material 15 as long as it has heat resistance to the heating by the heating means 24.
  • the layered structure of the alloy structure is performed on the surface to be formed of the base material 15 to form a shaped object in a state in which the base material 15 and the alloy structure are integrated. It will be obtained. Therefore, as the base material 15, the base material 15 having a suitable shape such as a flat plate can be used on the assumption that it is separated from the alloy structure by a cutting process or the like.
  • the prepared alloy powder 10 is spread on the surface to be shaped. That is, the alloy powder 10 is spread on the base material 15 placed on the layered modeling apparatus in the first powder spreading process in the layered modeling.
  • the spreading of the alloy powder 10 is, as shown in FIG. 1 (b), the alloy powder 10 (see FIG. 1 (a)) supplied on the processing table 22 by a powder feeder (not shown). It can carry out by sweeping so that it may pass on the surface (base material 15), and laying the alloy powder 10 in thin layers.
  • the thickness of the thin layer of the alloy powder 10 formed by spreading can be appropriately adjusted according to the output of the heating means for melting the alloy powder 10, the average particle diameter of the alloy powder 10, etc. Is in the range of about 10 ⁇ m to 1000 ⁇ m.
  • the expanded alloy powder 10 is locally heated and melted and then solidified, and the solidified layer is obtained by scanning the heated region by the local heating with respect to the plane on which the alloy powder 10 is expanded.
  • Shape 40 According to two-dimensional shape information obtained from three-dimensional shape information (such as 3D-CAD data) representing the three-dimensional shape of the alloy structure to be manufactured, the formation of the solidified layer 40 (see FIG. It is carried out by scanning the heated region by the heating means 24.
  • the two-dimensional shape information virtually divides the three-dimensional shape of the alloy structure to be manufactured by a predetermined thickness interval and virtually specifies the shape of each thin layer when divided into a plurality of thin layer groups. It is information. According to such two-dimensional shape information, a solidified layer 40 having a predetermined two-dimensional shape and thickness is formed.
  • the local heating of the alloy powder 10 is carried out by limiting the heated region on the spread alloy powder 10 by the heating means 24 as shown in FIG. This is performed by selectively melting the part so that a minute molten pool (melting part 20) is formed.
  • the size of the molten portion 20 formed by melting the alloy powder 10 is preferably 1 mm or less in diameter.
  • the region to be heated by the local heating of the alloy powder 10 is scanned so as to move parallel to the surface to be shaped, as shown in FIG. 1 (d).
  • the scanning of the heated region can be performed by scanning the irradiation spot of the heat source with a galvano mirror or the like in addition to scanning of the main body of the heating means 24, and it is performed by an appropriate method such as raster scanning.
  • overlap scanning with a plurality of radiation sources may be performed to flatten the irradiated energy density.
  • the molten portion 20 is cooled and solidified under the ambient temperature.
  • the solidified portion 30 formed by the solidification of the molten portion 20 forms a dense aggregate of the solidified portion 30 while being integrated with the base material and the solidified portion 30 already formed.
  • the scanning speed, output, energy density and scanning width of the heating means 24 are estimated from the elemental composition of the alloy powder 10, the particle size distribution, the material of the base 15, the positional relationship between the melting portion 20 and the solidification portion 30, chamber temperature etc. It may be adjusted appropriately based on heat conduction and heat radiation. Further, the cooling temperature for cooling the molten portion 20 may be set in consideration of dimensional change, thermal strain and the like according to the elemental composition of the alloy structure. By performing scanning while maintaining the size of the melting portion 20, the melting rate, the cooling rate, the time interval of melting and cooling, etc. in a predetermined range, the strength distribution of the shaped alloy structure is made uniform, It is possible to reduce residual stress and surface roughness.
  • melting and solidification of the alloy powder 10 are repeated on the base material 15 placed on the base material placement table 21 to form a set of solidification parts 30.
  • a solidified layer 40 having a predetermined two-dimensional shape and thickness is formed.
  • the base material mounting table 21 is solidified The height is lowered corresponding to the thickness of the layer 40 so that the new surface to be shaped of the upper surface of the solidified layer 40 is flush with the upper surface of the processing table 22.
  • the powder spreading process is performed in the same manner as in FIGS. 1 (a) to 1 (b), and as shown in FIG. 1 (g), a new surface is formed on the upper surface of the solidified layer 40 already formed.
  • the supplied alloy powder 10 is spread.
  • the solidified layer shaping step is performed, and the solidified layer 40 of the next layer is laminated.
  • the solidified portion 30 to be laminated is integrated with a part of the lower solidified layer 40 to be densely sintered.
  • the powder spreading process and the solidified layer forming process with the upper surface of the formed solidified layer 40 as a surface to be shaped can be repeated to laminate and model the alloy structure having a desired shape and size.
  • shape forming processing and surface processing of the solidified portion 30 to the solidified layer 40 can be performed in a high temperature state until the solidified portion 30 is formed after the alloy powder 10 is melted. .
  • Such processing is performed, for example, in a metal or an alloy in a state where the surface temperature of the molten portion 30 to the solidified portion 40 is about 500 ° C. or higher, preferably 50% to 75% of the melting point (Tm) of the alloy. It can be carried out by processing using a tool made of an inorganic or inorganic composite material such as a diamond powder, an intermetallic compound powder, or a powder compact of tungsten carbide or the like. By such processing, it is possible to form or decorate an alloy structure that is difficult to work into a shape with higher precision.
  • a hot isostatic pressing (HIP) treatment may be separately performed on the alloy structure layered and shaped by repeating the powder spreading step and the solidified layer shaping step.
  • HIP hot isostatic pressing
  • the solidified structure of the alloy structure may be made more compact or defects of the solidified structure may be removed in some cases.
  • each elemental composition of the minute solidified structure (solidified portion 30) well reflects the elemental composition of the used alloy powder, so uniformity of elemental composition distribution and uniformity of mechanical strength distribution A high solid solution phase can be formed.
  • a solidified structure (solidified portion 30) is formed by heating from one direction, and the crystal growth direction is oriented substantially in one direction ( Since the solidified layer 40) can be stacked, an alloy structure with high anisotropy can be formed.
  • FIG. 2 is a cross-sectional view schematically showing the metal structure of the alloy structure.
  • (A) is a cross-sectional view of the alloy structure according to the present embodiment,
  • (b) is an enlarged cross-sectional view of part A in (a)
  • (c) is a schematic view of the metal structure of the alloy material according to the comparative example. It is sectional drawing which showed.
  • the alloy structure 1 has a metal structure derived from the above-described manufacturing method by lamination molding, and a solidified structure (solidified structure formed by solidification of a melted alloy) It consists of a set of parts 30).
  • a part of the alloy structure manufactured by lamination molding is extracted, and the cross section is shown.
  • Each solidified structure (solidified portion 30) has a substantially hemispherical original shape derived from the contour shape of the molten pool (melted portion 20) by local heating, and is integrated with other solidified portions 30 in the periphery. It forms a fine metal structure.
  • the solidified portions 30 are arranged in a two-dimensional manner, with the arc side facing in the same direction, so that a layered solidified layer 40 formed of a set of solidified portions 30 is formed. Then, by laminating a large number of solidified layers 40 formed in this manner, a metal structure in which solidified portions 30 are three-dimensionally arranged is formed.
  • the solidified portion 30 forming the solidified layer 40 may be integrated with other solidified portions 30 around the same layer, or the chord side of each solidified portion 30 Because it may be integrated with the other solidified layer 40 laminated, the substantially hemispherical original shape of the solidified portion or the melting boundary 100 between the solidified portions 30 may not be observed in the solidified structure. .
  • the alloy structure 1 uses as main crystals columnar crystals in which at least Al, Co, Cr, Fe and Ni are solid-solved.
  • FIG. 2B the cross section of the metallographic structure of the alloy structure is shown enlarged to a viewing angle of several hundred ⁇ m to several mm.
  • Each crystal grain 50 contained in the metal structure of the alloy structure grows epitaxially with the crystal orientation substantially along the stacking direction of the solidified layer 40, and the grain boundary 110 (high angle grain boundary) is oriented in the stacking direction A structure is produced which extends beyond the melting boundary 100 between the solidified portions 30 while being oriented.
  • Each crystal grain 50 may be refined to an average crystal grain size of 10 ⁇ m or less.
  • the refined crystal grains 50 maintain the crystal orientation, and the low angle grain boundary 120 may be observed inside the area divided into the high angle grain boundaries 110.
  • the small angle grain boundary 120 has an inclination angle of 15 Grain boundaries of degree or less, high angle grain boundaries 110 are defined as grain boundaries having a tilt angle of more than 15 °.
  • the refined crystal grains 50 tend to be an aggregation of crystal grains having a small twist angle as well as a tilt angle.
  • the conventional high entropy alloy material (the alloy material according to the comparative example) has a metal structure derived from the manufacturing method by casting.
  • the alloy material according to the comparative example as shown in FIG. 2C, isotropically extending grain boundaries 110 are recognized, and coarse equiaxed crystal grains having an average crystal grain size exceeding 100 ⁇ m are formed.
  • the cross section of the metallographic structure of the alloy material is enlarged and shown at a viewing angle of several hundred ⁇ m to several mm.
  • the alloy material according to the comparative example segregation is likely to occur as the nuclei grow, the uniformity of the composition distribution is lowered, or the crystal grains are coarse, so that the stress is difficult to be dispersed, and the surface causing cleavage or slip is long As a result, the mechanical strength is not sufficient.
  • the solid solution phase can not grow well, there is a problem that the size is small and a complicated shape can not be formed.
  • the alloy structure according to the present embodiment since crystals having relatively uniform crystal orientation are epitaxially grown, and consist of aggregates of crystal grains 50 grown favorably in the same environment, the alloy powder is adjusted The elemental composition thus obtained is easily maintained regardless of the shape and size of the alloy structure, and the uniformity of the composition distribution is enhanced.
  • the crystal grains 50 are miniaturized, strain due to stress is not easily concentrated locally, and the uniformity of mechanical strength is enhanced.
  • the surface which produces cleavage and slip becomes short, it is advantageous at the point which mechanical strength improves.
  • the crystal growth direction is oriented and anisotropy is increased, it is also effective in using direction strength and magnetic characteristics.
  • FIG. 3 is a schematic flow chart showing an example of a method of producing an alloy powder used as a raw material of an alloy structure.
  • the various properties of the alloy structure according to the present embodiment are likely to reflect the influence of the elemental composition of the alloy powder used in additive manufacturing. Therefore, it is preferable to make the alloy powder used as a raw material into an elemental composition in which the concentration of unavoidable impurities is reduced, and as a method of manufacturing the alloy powder, vacuum carbon deoxidation capable of manufacturing an alloy with high cleanliness. It is a preferable form to use a manufacturing method by complex refining using a method.
  • the manufacturing method of the alloy powder shown in FIG. 3 is that the degree of cleanliness is improved by performing out-of-core refining using a ladle and using the crude metal as the raw metal for the composite smelting using a vacuum carbon deoxidation method. It is a method of refining a high alloy and preparing an alloy powder using the alloy, which is a method which can be applied as a process of preparing the above-mentioned alloy powder.
  • the electric furnace 301 performs a melting process to melt the metal lump 302 of the rough metal which is a raw material of the alloy powder.
  • the electric furnace 301 is a three-phase AC arc furnace including an electrode 304 such as a carbon electrode for generating arc discharge in the furnace and an oxygen burner 305 for blowing oxygen gas into the furnace.
  • an electrode 304 such as a carbon electrode for generating arc discharge in the furnace
  • an oxygen burner 305 for blowing oxygen gas into the furnace.
  • metal scraps, scrap metal, etc. can be used as the metal mass 302 .
  • the type of the metal mass 302 be blended so as to have an elemental composition compatible with the alloy powder to be manufactured, and that a type with few impurity elements be selected in advance.
  • the metal block 302 is placed in the furnace of the electric furnace 301, and an arc discharge 303 is generated between the electrode 304 and the metal block 302, thereby forming the metal block 302. Is melted and made into molten metal 310.
  • the oxygen gas 306 is blown into the molten metal 310 by the oxygen burner 305 to perform a peroxidation treatment to form a slag.
  • impurity elements such as Si, Mn, and P contained in the molten metal 310 can be transferred as oxides into the slag.
  • the molten metal 310 is discharged from the outlet port 308 of the electric furnace 301 and transferred to the ladle 309 as shown in FIG. 3 (c).
  • the slag containing a large amount of impurity elements floated on the liquid surface of the molten metal 310 separates the molten metal 310 and the slag so as not to transfer to the ladle 309, and the concentration of impurity elements such as Si, Mn, P etc.
  • a reduced melt 310 is obtained.
  • the molten metal 310 is tapped from the bottom of the ladle 309 and transferred to the ladle refining furnace 311.
  • the ladle smelting furnace 311 has a porous plug 313 at the bottom, and argon bubbling is performed by supplying argon gas 314 from the gas supply unit (not shown) into the furnace through the porous plug 313. There is.
  • argon bubbling the molten metal 310 transferred to the ladle smelting furnace 311 is homogenized by stirring, and impurity elements such as O and N are degassed.
  • the primary heat treatment of the molten metal 310 is performed.
  • the molten metal 310 transferred to the ladle smelting furnace 311 is heated by generating an arc discharge with the electrode 304 and continuously performing bottom bubbling argon bubbling through the porous plug 313, thereby the elemental component and the temperature are reduced. It can be made uniform.
  • the molten metal 310 is degassed using a vacuum degassing apparatus 316.
  • the inside of the vacuum degassing apparatus 316 is depressurized through an exhaust hole 317 to which a vacuum pump (not shown) is connected, and the molten metal 310 is sucked by moving relative to the ladle refining furnace 311 up and down. , And the apparatus for degassing the gas contained in the molten metal 310.
  • a vacuum pump not shown
  • a DH vacuum degassing furnace (Dortmund Horde type) having one immersion pipe is schematically shown as the vacuum degassing apparatus 316, but a shroud without the immersion pipe is made of a ladle It may be in the form of covering the smelting furnace 311, RH vacuum degassing furnace (Ruhrstahl Heraeus type), R It is also possible to take the form of an H injection furnace.
  • the gas of the impurity element degassed from the molten metal 310 can be efficiently exhausted by performing argon bubbling while reducing the gas phase atmosphere in the apparatus by the vacuum degassing apparatus 316. it can.
  • the molten metal 310 is heated by a heater (not shown) to prevent a decrease in temperature, and a powder for desulfurization is appropriately injected into the molten metal 310.
  • a heater not shown
  • the molten metal 310 in which the concentration of impurity elements such as S, O, H and the like is reduced can be obtained.
  • the secondary heat treatment of the molten metal 310 is performed.
  • the elemental composition and temperature of the molten metal 310 are finally adjusted.
  • the molten metal 310 of the ladle refining furnace 311 is subjected to a casting process.
  • the molten metal 310 is discharged from the bottom of the ladle refining furnace 311 and transferred to the tundish 318, and the impurity element is separated as slag in the tundish 318.
  • the molten metal 310 is poured from the bottom of the tundish 318 and poured into a mold 321 installed in the vacuum vessel 319.
  • a vacuum pump (not shown) is connected to the vacuum vessel 319 via the exhaust hole 320 so that the inside of the vessel in which the mold 321 is installed is made into a reduced pressure atmosphere.
  • an alloy block 322 having an arbitrary shape is cast.
  • an alloy in which the concentration of impurity elements such as N, O and H is reduced can be obtained.
  • the alloy refined by the above method can be used as a metal for preparing an alloy powder used in a powder preparation process.
  • the composite smelting using vacuum carbon deoxidation method results in an alloy with high purity in which the concentration of impurity elements is reduced, so that it is composed of particles with high uniformity of the elemental composition distribution, and the elemental composition between particles is The uniformity is also suitable for preparing an alloy powder with high uniformity. From the viewpoint of maintaining the cleanliness of the alloy refined in this manner, it is preferable to perform powdering treatment using a vacuum carbon deoxidation method when preparing the alloy powder.
  • the powderization process using a vacuum carbon deoxidation method can be performed using a vacuum furnace 324 to which a gas atomizer is directly connected as shown in FIG. 3 (i).
  • the vacuum furnace 324 is an electric furnace provided with an electrode 304 for generating arc discharge in the furnace, a gas injection lance (not shown) for blowing argon gas into the furnace, and an exhaust hole (not shown) to which a vacuum pump is connected. Be done.
  • a nozzle 328 is provided, and below the nozzle 328, an atomizing chamber 330 is provided so as to airtightly cover the outlet of the nozzle 328.
  • a gas injection hole 329 for blowing an inert gas such as argon gas to the molten metal 326 flowing down from the nozzle 328 is provided.
  • the alloy obtained by the complex refining described above is introduced into the furnace, and an arc discharge is generated between the electrode 304 and the alloy to form a molten metal 326 of the alloy.
  • the temperature of the molten metal 326 heated is a temperature range which exceeds 1600 degreeC and is 2500 degrees C or less.
  • the molten metal 326 is degassed while performing argon bubbling under a reduced pressure atmosphere by a vacuum pump connected to an exhaust hole (not shown), and the concentration of impurity elements such as N, O and H is further reduced. .
  • the molten metal 326 in a degassed state and in which the cleanliness is maintained flows downward from the nozzle 328.
  • the molten metal 328 which has flowed down is atomized by spraying an inert gas jetted from the gas injection holes 329 and solidified in the atomizing chamber 330 to be a powder 331 and accumulated at the bottom.
  • the vacuum furnace 324 may be a heat-resistant and refractory heating furnace so as to melt a high entropy alloy having a relatively high melting point, and the furnace wall may be a water-cooled type or the like.
  • a furnace wall of the vacuum furnace 324 for example, graphite (graphite), quartz (SiO 2 ), alumina (Al 2 O 3 ), magnesia (MgO), Al 2 O 3 ⁇ SiO 2 ⁇ Fe 2 O 3 ⁇ Na 2
  • FIG. 4 is a diagram showing an example of the change in concentration of impurity elements in an alloy powder prepared using a vacuum carbon deoxidation method.
  • the period B3 corresponding to f) and corresponding to the elapsed time 6.5 h to 8.2 h corresponds to the secondary heat treatment (see FIG. 3 (g)) in the ladle smelting furnace 311, and the elapsed time 8.
  • the C period corresponding to 2 h or later corresponds to the degassing process (see FIG. 3I) in the vacuum furnace 324.
  • P, Si, S, Sn, Sb, As, and the like can be appropriately adjusted by appropriately adjusting the number of times of slag separation, the time of degassing treatment, and the like in the process of preparing the alloy powder using the vacuum carbon deoxidation method. It is possible to limit the concentration of impurity elements such as Mn, O and N to a desired range.
  • the alloy structure according to the present embodiment described above can be applied as a structural member, a mechanical member, and the like.
  • the shape can be any shape within the layer-formable range, and the length dimension can exceed 70 mm and the volume can exceed 5495 mm 3 . It can be used for applications in severe environments such as high temperature environments, high radiation dose environments, and highly corrosive environments as well as applications in ordinary environments.
  • the invention can be suitably used for applications which are left in a high temperature environment for a long time.
  • the present invention includes, for example, structural materials for plants including casings, pipes, valves, etc., structural materials for generators, structural materials for nuclear reactors, structural materials for aerospace, members for hydraulic equipment, turbine blades, etc.
  • the present invention can be used for applications such as members for turbines, members for boilers, members for engines, members for nozzles, mechanical members for bearings, pistons, and the like.
  • the alloy structure according to the present embodiment is applied so as to cover the surface of a structure made of metal or alloy, such as a structural member or a mechanical member, whereby a heat resistant coating, a corrosion resistant coating, a wear resistant coating, It can also be used as a diffusion barrier layer or the like that serves as a barrier to atomic diffusion.
  • friction stir welding It can be applied to tools such as processing tools for on-stir welding (FSW), and is suitably used for a wide range of applications including friction stir welding of iron-based materials that require high high-temperature strength and wear resistance. it can.
  • alloy structures according to Examples 1-1 to 1-4 and Examples 2-1 to 2-3 are manufactured, and observation of solidified structure, distribution of elemental composition, mechanical The characteristics were evaluated.
  • alloy structures according to Comparative Examples 1-1 to 1-4 and Comparative Examples 2-1 to 2-4 were manufactured and evaluated together.
  • Example 1-1 As Example 1-1, an alloy structure having an elemental composition represented by Al 0.3 CoCrFeNi was manufactured by lamination molding.
  • the atomic concentration ratio is approximately 7 at% of the atomic concentration of Al, Co, Cr And the atomic concentration of Fe and Ni is about 23.3 at%.
  • an alloy powder was prepared by gas atomization using an alloy having an atomic concentration of Al of about 7 at% and an atomic concentration of Co, Cr, Fe, and Ni of about 23.3 at% as a base metal. Then, the obtained alloy powder was classified, and the particle size distribution was limited to the range of 50 ⁇ m to 100 ⁇ m, and the volume-based average particle size was about 70 ⁇ m.
  • the layered structure forming apparatus was used to form an alloy structure on the substrate.
  • a 100 mm ⁇ 100 mm ⁇ 10 mm plate-like carbon steel for machine structure “S45C” was used as a substrate.
  • an electron beam fusion lamination molding apparatus “A2X using a heat source as an electron beam” (Manufactured by Arcam) was used.
  • a cylindrical alloy structure having a diameter of 10 mm and a height of 50 mm was manufactured by repeatedly performing a powder spreading process and a solidified layer forming process on a base material in a vacuum atmosphere. At this time, melting of the alloy powder is the melting point of the alloy ( Pre-heating was performed at a temperature of 50% to 80% of Tm) in advance to suppress scattering of the spread alloy powder. The alloy structure was then separated from the substrate.
  • Embodiment 1-2 As Example 1-2, an alloy structure having an elemental composition represented by AlCoCrFeNi was manufactured by lamination molding.
  • the atomic concentration ratio is such that the atomic concentrations of Al, Co, Cr, Fe and Ni are about 20.0 at%.
  • Example 1-2 The alloy structure according to Example 1-2 was manufactured in the same manner as Example 1-1 except that the composition of the base metal used to prepare the alloy powder was changed.
  • Comparative Example 1-1 As Comparative Example 1-1, an alloy structure having an elemental composition represented by Al 0.3 CoCrFeNi was manufactured by casting. The atomic concentration ratio is about 7 at% of Al and about 23.3 at% of Co, Cr, Fe, and Ni.
  • an alloy powder was prepared by gas atomization using an alloy having an atomic concentration of Al of about 7 at% and an atomic concentration of Co, Cr, Fe, and Ni of about 23.3 at% as a base metal. Then, the obtained alloy powder was classified, and the particle size distribution was limited to the range of 50 ⁇ m to 100 ⁇ m, and the volume-based average particle size was about 70 ⁇ m.
  • the obtained alloy powder is put into an alumina crucible, melted by high frequency induction heating in a vacuum atmosphere, poured into a water-cooled mold made of copper, cooled and solidified to obtain a diameter.
  • a cylinder-shaped alloy structure of 10 mm and 50 mm in height was manufactured.
  • Comparative Example 1-2 As Comparative Example 1-2, an alloy structure having an elemental composition represented by Al 0.2 CoCrFeNi was manufactured by lamination molding. The atomic concentration ratio is about 4.8 at% for Al and about 23.8 at% for Co, Cr, Fe and Ni.
  • the alloy structure according to Comparative Example 1-2 was manufactured in the same manner as Example 1-1 except that the composition of the base metal used to prepare the alloy powder was changed.
  • Embodiment 1-3 As Example 1-3, an alloy structure having an elemental composition represented by Al 1.5 CoCrFeNi was manufactured by lamination molding.
  • the atomic concentration ratio is approximately 27.2 at% of the atomic concentration of Al, Co
  • the atomic concentrations of Cr, Fe and Ni are about 18.2 at%.
  • an alloy powder was prepared by gas atomization using an alloy having an atomic concentration of Al of about 27.2 at% and an atomic concentration of Co, Cr, Fe, and Ni of about 18.2 at% as a base metal. Then, the obtained alloy powder was classified, and the particle size distribution was limited to a range of 20 ⁇ m to 50 ⁇ m, and the volume-based average particle size was about 30 ⁇ m.
  • the laminate molding apparatus was used to model the alloy material on the base material.
  • a base material carbon steel "S45C” for cylinder-like machine structure for diameter 10 mm and height 50 mm was used.
  • the laser fusion lamination molding apparatus "EOSINT which made the heat source the laser beam. M270 "(manufactured by EOS) was used.
  • a 200 ⁇ m multilayer film-like alloy material was manufactured by repeatedly performing the powder spreading process and the solidified layer forming process on the base material in a nitrogen atmosphere.
  • Comparative Example 1-3 As Comparative Example 1-3, an alloy structure having an elemental composition represented by AlCoCrFeNi was produced by thermal spraying.
  • the atomic concentration ratio is about 20 atomic concentrations of Al, Co, Cr, Fe and Ni. . It is 0 at%.
  • each metal powder of Al, Co, Cr, Fe and Ni was mixed such that the atomic concentration of Al, Co, Cr, Fe and Ni was about 20.0 at%.
  • each metal powder was classified, and while limiting particle diameter distribution to the range of 50 micrometers or more and 150 micrometers or less, it was made for the average particle diameter on a volume basis to be about 70 micrometers.
  • the mixed metal powder was sprayed onto the base material by plasma spraying under a nitrogen atmosphere to produce a 200 ⁇ m film-like alloy structure.
  • a base material carbon steel "S45C" for machine-structure-use cylindrical shape with a diameter of 100 mm and a height of 10 mm was used.
  • Comparative Example 1-4 As Comparative Example 1-4, an alloy structure having an elemental composition represented by Al 2.0 CoCrFeNi was manufactured by lamination molding. The atomic concentration ratio is approximately 33.3 at% of the atomic concentration of Al, Co The atomic concentrations of Cr, Fe and Ni are about 16.7 at%.
  • the alloy structure according to Comparative Example 1-4 was manufactured in the same manner as Example 1-2 except that the composition of the base metal used for preparation of the alloy powder was changed.
  • Embodiment 1-4 As Example 1-4, an alloy structure whose elemental composition is represented by AlCoCrFeNiMo 0.5 was manufactured by lamination molding.
  • the atomic concentration ratio is such that the atomic concentrations of Al, Co, Cr, Fe and Ni are about 18.2 at% and the atomic concentration of Mo is about 9.1 at%.
  • an alloy powder was prepared by gas atomization using an alloy having an atomic concentration of Al, Co, Cr, Fe and Ni of about 18.2 at% and an atomic concentration of Mo of about 9.1 at% as a base metal. . Then, the obtained alloy powder was classified, and the particle size distribution was limited to the range of 50 ⁇ m to 100 ⁇ m, and the volume-based average particle size was about 70 ⁇ m.
  • the layered structure forming apparatus was used to form an alloy structure on the substrate.
  • a base material a cylindrical carbon steel for machine structure "S45C” with a diameter of 300 mm and a height of 10 mm was used.
  • an electron beam fusion lamination molding apparatus “A2X using a heat source as an electron beam” (Manufactured by Arcam) was used.
  • the layered molding apparatus manufactured a substantially cylindrical impeller-shaped alloy structure having a diameter of 300 mm and a height of 100 mm by repeatedly performing a powder spreading process and a solidified layer forming process on a base material in a vacuum atmosphere. . At this time, melting of the alloy powder was performed while performing preliminary heating at a temperature of 50% to 80% of the melting point (Tm) of the alloy in advance to suppress scattering of the spread alloy powder. Thereafter, the impeller-shaped alloy structure was separated from the substrate.
  • Example 2-1 As Example 2-1, an alloy structure represented by Al 0.3 CoCrFeNi and having a limited concentration of unavoidable impurities was manufactured by lamination molding.
  • the atomic concentration ratio is about 7 at% of Al and about 23.3 at% of Co, Cr, Fe, and Ni.
  • the concentration of P is 0.002 wt% or less
  • the concentration of Si is 0.010 wt% or less
  • the concentration of S is 0.001 wt% or less
  • the concentration of Sn is 0.002 wt% or less
  • the concentration of Sb is 0.001 wt%
  • the concentration of As was limited to 0.001 wt% or less
  • the concentration of O to 0.0003 wt% or less
  • the concentration of N to 0.001 wt% or less.
  • Example 2-1 The alloy structure according to Example 2-1 was manufactured in the same manner as Example 1-1 except that the composition of the base metal used for preparation of the alloy powder was changed.
  • Embodiment 2-2 As Example 2-2, an alloy structure having an elemental composition represented by AlCoCrFeNi and a limited concentration of unavoidable impurities was manufactured by lamination molding.
  • the atomic concentration ratio is such that the atomic concentrations of Al, Co, Cr, Fe and Ni are about 20.0 at%.
  • the concentration of P is 0.002 wt% or less
  • the concentration of Si is 0.010 wt% or less
  • the concentration of S is 0.001 wt% or less
  • the concentration of Sn is 0.002 wt% or less
  • the concentration of Sb is 0.001 wt%
  • the concentration of As was limited to 0.001 wt% or less
  • the concentration of O to 0.0003 wt% or less
  • the concentration of N to 0.001 wt% or less.
  • Example 2-2 The alloy structure according to Example 2-2 was manufactured in the same manner as Example 1-1 except that the composition of the base metal used for preparation of the alloy powder was changed.
  • Comparative Example 2-1 As Comparative Example 2-1, an alloy structure having an elemental composition represented by AlCoCrFeNi and a limited concentration of unavoidable impurities was manufactured by casting.
  • the atomic concentration ratio is such that the atomic concentrations of Al, Co, Cr, Fe and Ni are about 20.0 at%.
  • the concentration of P is 0.002 wt% or less
  • the concentration of Si is 0.010 wt% or less
  • the concentration of S is 0.001 wt% or less
  • the concentration of Sn is 0.002 wt% or less
  • the concentration of Sb is 0.001 wt%
  • the concentration of As was limited to 0.001 wt% or less
  • the concentration of O to 0.0003 wt% or less
  • the concentration of N to 0.001 wt% or less.
  • the alloy structure according to Comparative Example 2-1 was manufactured in the same manner as Comparative Example 1-1 except that the composition of the base metal used for preparing the alloy powder was changed.
  • Comparative Example 2-2 As Comparative Example 2-2, an alloy structure having an elemental composition represented by Al 0.2 CoCrFeNi and having a limited concentration of unavoidable impurities was manufactured by casting.
  • the atomic concentration ratio is about 4.8 at% for Al and about 23.8 at% for Co, Cr, Fe and Ni.
  • the concentration of P is 0.002 wt% or less
  • the concentration of Si is 0.010 wt% or less
  • the concentration of S is 0.001 wt% or less
  • the concentration of Sn is 0.002 wt% or less
  • the concentration of Sb is 0.001 wt%
  • the concentration of As was limited to 0.001 wt% or less
  • the concentration of O to 0.0003 wt% or less
  • the concentration of N to 0.001 wt% or less.
  • the alloy structure according to Comparative Example 2-2 was manufactured in the same manner as Example 1-1 except that the composition of the base metal used for preparation of the alloy powder was changed.
  • Example 2-3 As Example 2-3, an alloy structure represented by Al 1.5 CoCrFeNi and having a limited concentration of unavoidable impurities was manufactured by lamination molding.
  • the atomic concentration ratio is such that the atomic concentration of Al is about 27.2 at%, and the atomic concentrations of Co, Cr, Fe and Ni are about 18.2 at%.
  • the concentration of P is 0.005 wt% or less
  • the concentration of Si is 0.040 wt% or less
  • the concentration of S is 0.002 wt% or less
  • the concentration of Sn is 0.005 wt% or less
  • the concentration of Sb is 0.002 wt%
  • the concentration of As was limited to 0.005 wt% or less
  • the concentration of Mn to 0.050 wt% or less the concentration of O to 0.001 wt% or less
  • the concentration of N to 0.002 wt% or less.
  • the atomic concentration of Al is about 27.2 at%
  • the atomic concentrations of Co, Cr, Fe and Ni are about 18.2 at%
  • the concentration of P is 0.005 wt% or less
  • the concentration of Si is 0.040 wt%
  • the concentration of S is 0.002 wt% or less
  • the concentration of Sn is 0.005 wt% or less
  • the concentration of Sb is 0.002 wt% or less
  • the concentration of As is 0.005 wt% or less
  • the concentration of Mn is 0 .
  • An alloy powder was prepared by gas atomization using an alloy in which the concentration of 050 wt% or less, the concentration of O was limited to 0.001 wt% or less, and the concentration of N to 0.002 wt% or less was used as a metal. Then, the obtained alloy powder was classified, and the particle size distribution was limited to a range of 20 ⁇ m to 50 ⁇ m, and the volume-based average particle size was about 30 ⁇ m.
  • the laminate molding apparatus was used to model the alloy material on the base material.
  • a base material carbon steel "S45C” for machine-structure-use cylindrical shape with a diameter of 100 mm and a height of 10 mm was used.
  • the laser fusion lamination molding apparatus "EOSINT which made the heat source the laser beam. M270 "(manufactured by EOS) was used.
  • a 200 ⁇ m multilayer film-like alloy material was manufactured by repeatedly performing the powder spreading process and the solidified layer forming process on the base material in a nitrogen atmosphere.
  • Comparative Example 2-3 As Comparative Example 2-3, an alloy structure having an elemental composition represented by AlCoCrFeNi and a limited concentration of unavoidable impurities was manufactured by thermal spraying.
  • the atomic concentration ratio is such that the atomic concentrations of Al, Co, Cr, Fe and Ni are about 20.0 at%.
  • the concentration of P is 0.002 wt% or less
  • the concentration of Si is 0.010 wt% or less
  • the concentration of S is 0.001 wt% or less
  • the concentration of Sn is 0.002 wt% or less
  • the concentration of Sb is 0.001 wt%
  • the concentration of As was limited to 0.001 wt% or less
  • the concentration of O to 0.0003 wt% or less
  • the concentration of N to 0.001 wt% or less.
  • the atomic concentration of Al, Co, Cr, Fe and Ni is about 20.0 at%
  • the concentration of P is 0.002 wt% or less
  • the concentration of Si is 0.010 wt% or less
  • the concentration of S is 0.001 wt%
  • the concentration of Sn is 0.002 wt% or less
  • the concentration of Sb is 0.001 wt% or less
  • the concentration of As is 0.001 wt% or less
  • the concentration of Mn is 0.020 wt% or less
  • the concentration of O is 0.0003 wt%
  • metal powders of Al, Co, Cr, Fe and Ni in which the concentration of N is limited to 0.001 wt% or less were mixed.
  • each metal powder was classified, and while limiting particle diameter distribution to the range of 50 micrometers or more and 150 micrometers or less, it was made for the average particle diameter on a volume basis to be about 70 micrometers.
  • the mixed metal powder was sprayed onto the base material by plasma spraying under a nitrogen atmosphere to produce a 200 ⁇ m film-like alloy structure.
  • a base material carbon steel "S45C" for machine-structure-use cylindrical shape with a diameter of 100 mm and a height of 10 mm was used.
  • Comparative Example 2-4 As Comparative Example 2-4, an alloy structure in which the elemental composition was expressed as Al 2.0 CoCrFeNi and in which the concentration of unavoidable impurities was limited was manufactured by lamination molding.
  • the atomic concentration ratio is such that the atomic concentration of Al is about 33.3 at%, and the atomic concentrations of Co, Cr, Fe, and Ni are about 16.7 at%.
  • the concentration of P is 0.002 wt% or less
  • the concentration of Si is 0.010 wt% or less
  • the concentration of S is 0.001 wt% or less
  • the concentration of Sn is 0.002 wt% or less
  • the concentration of Sb is 0.001 wt%
  • the concentration of As was limited to 0.001 wt% or less
  • the concentration of O to 0.0003 wt% or less
  • the concentration of N to 0.001 wt% or less.
  • the alloy structure according to Comparative Example 2-4 was manufactured in the same manner as Example 2-2 except that the composition of the base metal used for preparation of the alloy powder was changed.
  • SEM-EDX scanning Electron Microscope-Energy Dispersive X-ray
  • the results of the observation of the solidified structure, the analysis of the nickel concentration distribution, and the hardness measurement are shown in Table 1.
  • the column of element composition in Table 1 indicates the atomic concentration ratio of the main component element to the additive element.
  • ⁇ indicates an example in which the unavoidable impurities are not limited, an example in which “-” slightly restricts the inevitable impurities, and “-” indicates an example in which the inevitable impurities are more restricted.
  • the column of "Crystal structure” indicates the crystal structure of the main crystal. “*” In the “hardness” column indicates that a crack has occurred.
  • the alloy structures according to Examples 1-1 to 1-4 and Examples 2-1 to 2-3 have the crystal structure or body-centered cubic lattice of the face-centered cubic lattice. It was confirmed to have any of the crystal structures of Further, it is understood from the values of the nickel concentration distribution and the hardness that the standard deviation is small and the uniformity of the distribution of the elemental composition and the mechanical strength is high. Further, from the observation of the solidified structure, a solidified structure and a crystal structure as shown in FIGS. 2 (a) and 2 (b) were confirmed.
  • the values of the nickel concentration distribution and the hardness have a large standard deviation, and the elements It can be seen that the uniformity of the composition and the distribution of mechanical strength is low. In addition, it was recognized that the crystal structure reflects the low uniformity of the elemental composition, and a multiphase structure is formed. In particular, when the atomic concentration of Al is lowered, the hardness remains lower than that of mild steel, and it has been found that it is unsuitable as a structural member, a mechanical member or the like. In addition, when the atomic concentration of Al was increased, a B2 type intermetallic compound was formed, and a crack was generated at the time of the test, which proved to be unsuitable as a structural member, a mechanical member or the like.
  • Example 3-1 and Example 3-2 were manufactured, and stress-strain characteristics were evaluated.
  • FIG. 5 is a view showing the shape and dimensions of the alloy structure according to the third embodiment.
  • Example 3-1 As Example 3-1, an alloy structure shown in FIG. 5 in which the elemental composition is expressed as AlCoCrFeNi and the concentration of unavoidable impurities is limited was manufactured by lamination molding.
  • the atomic concentration ratio is Al
  • the atomic concentration of Co, Cr, Fe and Ni is about 20.0 at%.
  • the concentration of P is 0 . 002 wt% or less, Si concentration 0.010 wt% or less, S concentration 0.001 wt% or less, Sn concentration 0.002 wt% or less, Sb concentration 0.001 wt% or less, As concentration 0.1.
  • the concentration of 001 wt% or less, the concentration of Mn was 0.020 wt% or less, the concentration of O was 0.0003 wt% or less, and the concentration of N was 0.001 wt% or less.
  • the atomic concentration of Al is about 7 at%
  • the atomic concentrations of Co, Cr, Fe and Ni are about 23.3 at%
  • the concentration of P is 0.002 wt% or less
  • the concentration of Si is 0.010 wt% or less
  • the concentration of S is 0.001 wt% or less
  • the concentration of Sn is 0.002 wt% or less
  • the concentration of Sb is 0.001 wt% or less
  • the concentration of As is 0.001 wt% or less
  • the concentration of Mn is 0.020 wt% or less
  • An alloy powder was prepared by gas atomization using an alloy in which the concentration of O was limited to 0.0003 wt% or less and the concentration of N to 0.001 wt% or less as a metal. Then, the obtained alloy powder was classified, and the particle size distribution was limited to a range of 45 ⁇ m to 105 ⁇ m, and the volume-based average particle size was about 70 ⁇ m.
  • the laminate molding apparatus was used to model the alloy material on the base material.
  • a plate-like carbon steel for machine structure "S45C" of 200 mm ⁇ 200 mm ⁇ 10 mm was used.
  • an electron beam melting lamination molding apparatus “A2X” (where the heat source is an electron beam) Arcam) was used.
  • a plate-shaped object of 150 mm ⁇ 150 mm ⁇ 30 mm (a plate-like structure (plate shape) as shown in FIG. 5 by repeatedly performing a powder spreading step and a solidified layer forming step on a substrate under a vacuum atmosphere.
  • Parts were formed, and a total of 16 28 mm ⁇ 28 mm ⁇ 20 mm rectangular parallelepiped shaped objects (rectangular parallelepiped parts) were formed at intervals of 6 mm in length and width.
  • melting of the alloy powder was carried out while performing preliminary heating at a temperature of 50% to 80% of the melting point (Tm) of the alloy powder in advance to suppress scattering of the spread alloy powder.
  • Tm melting point
  • the volume of the whole modeling thing was 925880 mm 3 .
  • Example 3-2 As Example 3-2, an alloy structure shown in FIG. 5 in which the elemental composition is represented by AlCoCrFeNi and the concentration of unavoidable impurities is not limited was manufactured by lamination molding.
  • the atomic concentration ratio is such that the atomic concentrations of Al, Co, Cr, Fe and Ni are about 20.0 at%.
  • the alloy structure according to Example 3-2 was manufactured in the same manner as Example 3-1 except that the composition of the base metal used to prepare the alloy powder was changed.
  • the concentration of unavoidable impurities in the alloy powder is 0.008 wt% of P, 0.040 wt% of Si, 0.012 wt% of S, and 0.006 wt% of Sn.
  • the concentration was 0.002 wt%
  • the concentration of As was 0.006 wt%
  • the concentration of Mn was 0.300 wt%
  • the concentration of O was 0.002 wt%
  • the concentration of N was 0.003 wt%.
  • Example 3-1 and Example 3-2 analysis of nickel concentration distribution was performed.
  • the analysis of the nickel concentration distribution is performed by scanning electron microscope-energy dispersive X-ray spectroscopy (Energy dispersive X-ray spectroscopy) for each of the 16 rectangular parallelepipeds in total.
  • the measurement was carried out by measuring the nickel concentration in 10 randomly extracted areas using a dispersive X-ray Detector (SEM-EDX).
  • SEM-EDX dispersive X-ray Detector
  • test piece was extract
  • the test piece is a dumbbell-shaped test piece whose major axis is the stacking direction in the alloy structure, which is cut out from each rectangular parallelepiped portion to the plate-like portion, and the size of the parallel portion is 4 mm in diameter ⁇ 30 mm in height. It was.
  • the measurement results of the compression true stress-compression true strain diagram at room temperature are shown in FIG. 6 as an average for a total of 16 rectangular portions.
  • FIG. 6 is a compression true stress-compression true strain diagram in the alloy structure according to the third embodiment.
  • Example 3-1 and Example 3-2 the variation of the true stress-true strain diagram is hardly recognized in any of Example 3-1 and Example 3-2, and the line width diagram shown in FIG. 6 is drawn. did it. That is, in the alloy structure having a volume about 160 times or more larger than that of the alloy material shown in Non-Patent Document 2, it has been confirmed that the uniformity of the mechanical characteristics is enhanced over the entire region of the shaped object.
  • the tensile strength is about 2800 MPa and the total elongation is about 38% in Example 3-2
  • the tensile strength is about 3850 MPa and the total elongation is about 43% in Example 3-1.
  • Strength is about 1 . It can be seen that the total elongation has increased about 1.1 times by 37 times. Therefore, it is recognized that mechanical properties can be further improved by reducing the concentration of unavoidable impurities.
  • Example 4-1 As Example 4-1, an alloy structure represented by AlCoCrFeNi and having a limited concentration of unavoidable impurities was manufactured by lamination molding.
  • the atomic concentration ratio is such that the atomic concentrations of Al, Co, Cr, Fe and Ni are about 20.0 at%.
  • the concentration of P is 0.002 wt% or less
  • the concentration of Si is 0.010 wt% or less
  • the concentration of S is 0.001 wt% or less
  • the concentration of Sn is 0.002 wt% or less
  • the concentration of Sb is 0.001 wt%
  • the concentration of As was limited to 0.001 wt% or less
  • the concentration of O to 0.0003 wt% or less
  • the concentration of N to 0.001 wt% or less.
  • the atomic concentration of Al is about 7 at%
  • the atomic concentrations of Co, Cr, Fe and Ni are about 23.3 at%
  • the concentration of P is 0.002 wt% or less
  • the concentration of Si is 0.010 wt% or less
  • the concentration of S is 0.001 wt% or less
  • the concentration of Sn is 0.002 wt% or less
  • the concentration of Sb is 0.001 wt% or less
  • the concentration of As is 0.001 wt% or less
  • the concentration of Mn is 0.020 wt% or less
  • An alloy powder was prepared by gas atomization using an alloy in which the concentration of O was limited to 0.0003 wt% or less and the concentration of N to 0.001 wt% or less as a metal. Then, the obtained alloy powder was classified, and the particle size distribution was limited to a range of 45 ⁇ m to 105 ⁇ m, and the volume-based average particle size was about 70 ⁇ m.
  • the layered structure forming apparatus was used to form an alloy structure on the substrate.
  • a base material a plate-like carbon steel for machine structure "S45C" of 200 mm ⁇ 200 mm ⁇ 10 mm was used.
  • an electron beam fusion lamination molding apparatus “A2X using a heat source as an electron beam” (Manufactured by Arcam) was used.
  • the dumbbell-shaped test piece whose horizontal axis is the stacking direction of the solidified layer is formed as an alloy structure did.
  • the dumbbell-shaped test piece was shaped in a state of being placed horizontally on the base together with the support member for supporting the test piece main body, and the parallel portion was made to have a diameter of 4 mm ⁇ height 30 mm.
  • Embodiment 4-2 As Example 4-2, an alloy structure having an elemental composition represented by AlCoCrFeNi and a limited concentration of unavoidable impurities was manufactured by lamination molding.
  • the atomic concentration ratio is such that the atomic concentrations of Al, Co, Cr, Fe and Ni are about 20.0 at%.
  • the concentration of P is 0.002 wt% to 0.005 wt%, the concentration of Si 0.010 wt% to 0.040 wt%, the concentration of S 0.001 wt% to 0.002 wt%, the concentration of Sn 0..
  • the alloy structure according to Example 4-2 was manufactured in the same manner as Example 4-1 except that the composition of the base metal used for preparation of the alloy powder was changed.
  • Example 4-3 As Example 4-3, an alloy structure represented by AlCoCrFeNi and not limiting the concentration of unavoidable impurities was manufactured by lamination molding.
  • the atomic concentration ratio is such that the atomic concentrations of Al, Co, Cr, Fe and Ni are about 20.0 at%.
  • the alloy structure according to Example 4-3 was manufactured in the same manner as Example 4-1 except that the composition of the base metal used for preparation of the alloy powder was changed.
  • the concentration of unavoidable impurities in the alloy powder is 0.008 wt% of P, 0.040 wt% of Si, 0.012 wt% of S, and 0.006 wt% of Sn.
  • the concentration was 0.002 wt%
  • the concentration of As was 0.006 wt%
  • the concentration of Mn was 0.300 wt%
  • the concentration of O was 0.002 wt%
  • the concentration of N was 0.003 wt%.
  • FIG. 7 is a view showing test temperature dependency of tensile strength in the alloy structure according to Example 4.
  • the alloy structures according to Examples 4-1 to 4-2 in which the unavoidable impurities are limited the alloy structures according to Example 4-3 in which the unavoidable impurities are not limited.
  • the tensile strength is improved.
  • the tensile strength is improved in a wide temperature range. Therefore, it has been confirmed that it is effective to further improve the mechanical characteristics by reducing the concentration of unavoidable impurities.

Landscapes

  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Manufacturing & Machinery (AREA)
  • Chemical & Material Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Optics & Photonics (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Powder Metallurgy (AREA)

Abstract

L'invention concerne une structure d'alliage ayant une composition élémentaire et une répartition de résistance mécanique hautement homogènes, ayant une bonne résistance à haute température et une bonne résistance à la corrosion, et ayant des dimensions de forme définies de façon arbitraire. Cette structure d'alliage contient de l'Al, Co, Cr, Fe, et Ni, chacun étant présent selon une concentration atomique comprise entre 5 à 30 % at, la différence entre les concentrations atomiques d'au moins quatre des éléments mentionnés ci-dessus étant dans la plage de moins de 3 % at, et un cristal en colonne formé par dissolution des cinq éléments mentionnés ci-dessus constituant le cristal principal.
PCT/JP2015/070470 2014-07-23 2015-07-17 Structure d'alliage et procédé de production de structure d'alliage. Ceased WO2016013496A1 (fr)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP2014150020A JP6459272B2 (ja) 2014-07-23 2014-07-23 合金構造体
JP2014-150020 2014-07-23
JP2014151331A JP6443721B2 (ja) 2014-07-25 2014-07-25 合金構造体の製造方法
JP2014-151331 2014-07-25

Publications (1)

Publication Number Publication Date
WO2016013496A1 true WO2016013496A1 (fr) 2016-01-28

Family

ID=55163022

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2015/070470 Ceased WO2016013496A1 (fr) 2014-07-23 2015-07-17 Structure d'alliage et procédé de production de structure d'alliage.

Country Status (1)

Country Link
WO (1) WO2016013496A1 (fr)

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN112195463A (zh) * 2020-07-31 2021-01-08 中北大学 一种激光熔覆AlCoCrFeNi/NbC梯度高熵合金涂层材料及方法
CN112746214A (zh) * 2020-12-29 2021-05-04 中南大学 一种双相高熵合金及其制备方法
CN113210629A (zh) * 2021-05-21 2021-08-06 大连理工大学 一种AlCoCrFeNi2.1共晶高熵合金及其激光选区增材制造制备方法
CN113318733A (zh) * 2021-05-28 2021-08-31 清华大学 一种高熵纳米酶的制备方法及其应用
CN113878948A (zh) * 2021-09-27 2022-01-04 大连理工大学 一种大尺寸共晶高熵合金及其制备方法和应用
CN116479303A (zh) * 2023-04-20 2023-07-25 哈尔滨工业大学 一种高温环境下应用的Al-Co-Cr-Fe-Ni-Ta系高强高熵合金及制备方法
CN116586813A (zh) * 2023-05-23 2023-08-15 西安理工大学 航空发动机外壳制造用药芯焊丝及航空外壳的制备方法

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2002173732A (ja) * 2000-11-29 2002-06-21 Univ Qinghua ハイエントロピー多元合金
JP2004124201A (ja) * 2002-10-04 2004-04-22 Japan Science & Technology Corp 金属粉末光造形方法
CN102220026A (zh) * 2011-04-11 2011-10-19 黄元盛 高熵合金粉末导电高分子复合材料及其制作方法
CN103056352A (zh) * 2012-12-04 2013-04-24 中国人民解放军装甲兵工程学院 用于超音速喷涂的高熵合金粉末材料及其制备方法
US20130323116A1 (en) * 2012-05-31 2013-12-05 Swe-Kai Chen Alloy material with constant electrical resistivity, applications and method for producing the same
JP2014105373A (ja) * 2012-11-29 2014-06-09 Canon Inc 金属光造形用金属粉末、射出成形用金型の製造方法、射出成形用金型および成形品

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2002173732A (ja) * 2000-11-29 2002-06-21 Univ Qinghua ハイエントロピー多元合金
JP2004124201A (ja) * 2002-10-04 2004-04-22 Japan Science & Technology Corp 金属粉末光造形方法
CN102220026A (zh) * 2011-04-11 2011-10-19 黄元盛 高熵合金粉末导电高分子复合材料及其制作方法
US20130323116A1 (en) * 2012-05-31 2013-12-05 Swe-Kai Chen Alloy material with constant electrical resistivity, applications and method for producing the same
JP2014105373A (ja) * 2012-11-29 2014-06-09 Canon Inc 金属光造形用金属粉末、射出成形用金型の製造方法、射出成形用金型および成形品
CN103056352A (zh) * 2012-12-04 2013-04-24 中国人民解放军装甲兵工程学院 用于超音速喷涂的高熵合金粉末材料及其制备方法

Non-Patent Citations (3)

* Cited by examiner, † Cited by third party
Title
BRIF, YEVGENI ET AL.: "The use of high-entropy alloys in additive manufacturing", SCRIPTA MATERIALIA, vol. 99, pages 93 - 96 *
KUNCE, I. ET AL.: "Structure and hydrogen storage properties of a high entropy ZrTiVCrFeNi alloy synthesized using Laser Engineered Net Shaoing(LENS", INTERNATIONAL JOURNAL OF HYDROGEN ENERGY, vol. 38, no. 27, pages 12180 - 12189, XP028694419, DOI: doi:10.1016/j.ijhydene.2013.05.071 *
WANG, F. J. ET AL.: "Cooling Rate and Size Effect on the Microstructure and Mechanical Properties of AlCoCrFeNi High Entropy Alloy", JOURNAL OF ENGINEERING MATERIALS AND TECHNOLOGY, vol. 131, no. 3, July 2009 (2009-07-01), pages 034501.1 - 034501.3 *

Cited By (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN112195463A (zh) * 2020-07-31 2021-01-08 中北大学 一种激光熔覆AlCoCrFeNi/NbC梯度高熵合金涂层材料及方法
CN112746214A (zh) * 2020-12-29 2021-05-04 中南大学 一种双相高熵合金及其制备方法
CN113210629A (zh) * 2021-05-21 2021-08-06 大连理工大学 一种AlCoCrFeNi2.1共晶高熵合金及其激光选区增材制造制备方法
CN113318733A (zh) * 2021-05-28 2021-08-31 清华大学 一种高熵纳米酶的制备方法及其应用
CN113318733B (zh) * 2021-05-28 2022-05-13 清华大学 一种高熵纳米酶的制备方法及其应用
CN113878948A (zh) * 2021-09-27 2022-01-04 大连理工大学 一种大尺寸共晶高熵合金及其制备方法和应用
CN116479303A (zh) * 2023-04-20 2023-07-25 哈尔滨工业大学 一种高温环境下应用的Al-Co-Cr-Fe-Ni-Ta系高强高熵合金及制备方法
CN116479303B (zh) * 2023-04-20 2024-05-07 哈尔滨工业大学 一种高温环境下应用的Al-Co-Cr-Fe-Ni-Ta系高强高熵合金及制备方法
CN116586813A (zh) * 2023-05-23 2023-08-15 西安理工大学 航空发动机外壳制造用药芯焊丝及航空外壳的制备方法

Similar Documents

Publication Publication Date Title
JP6388381B2 (ja) 合金構造体
JP6459272B2 (ja) 合金構造体
JP6393885B2 (ja) 合金粉末の製造方法
JP6455701B2 (ja) 合金構造体
WO2016013497A1 (fr) Structure en alliage, et procédé de fabrication de celle-ci
WO2016013498A1 (fr) Structure en alliage, et procédé de fabrication de celle-ci
JP6455699B2 (ja) 合金構造体の製造方法
Alshataif et al. Manufacturing methods, microstructural and mechanical properties evolutions of high-entropy alloys: a review
WO2016013495A1 (fr) Structure en alliage et procédé de fabrication de structure en alliage
JP6388277B2 (ja) 合金構造体の製造方法
Guo et al. Selective laser melting additive manufacturing of pure tungsten: Role of volumetric energy density on densification, microstructure and mechanical properties
JP6455700B2 (ja) 合金構造体の製造方法
WO2016013496A1 (fr) Structure d'alliage et procédé de production de structure d'alliage.
JP7116495B2 (ja) 高炭素コバルト系合金
WO2016013494A1 (fr) Poudre d'alliage utilisée dans la modélisation par dépôt fondu, et procédé de production de ladite poudre d'alliage
WO2016013492A1 (fr) Poudre d'alliage utilisée en dépôt de fil en fusion
JP2020114948A (ja) 金属積層造形用混合粉末
JP6536927B2 (ja) 合金構造体
JP6388278B2 (ja) 溶融積層造形に用いる合金粉末
JP6393884B2 (ja) 合金粉末の製造方法
JP6432822B2 (ja) 溶融積層造形に用いる合金粉末
JP7103548B2 (ja) Ｎｉ－Ｃｒ－Ｍｏ系合金部材、Ｎｉ－Ｃｒ－Ｍｏ系合金粉末、および、複合部材
WO2016013493A1 (fr) Procédé de production d'un alliage de coulée
JP6443721B2 (ja) 合金構造体の製造方法
Gamon Microstructure and Hardness Comparison of Inconel 625 Alloy of Various Additive Manufacturing Processes Following Heat Treatments

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 15825465

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 15825465

Country of ref document: EP

Kind code of ref document: A1