WO2020110498A1 - Powder for laminate formation use, laminated article, and method for producing laminated article - Google Patents

Powder for laminate formation use, laminated article, and method for producing laminated article Download PDF

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WO2020110498A1
WO2020110498A1 PCT/JP2019/040856 JP2019040856W WO2020110498A1 WO 2020110498 A1 WO2020110498 A1 WO 2020110498A1 JP 2019040856 W JP2019040856 W JP 2019040856W WO 2020110498 A1 WO2020110498 A1 WO 2020110498A1
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mass
less
iron
powder
based alloy
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PCT/JP2019/040856
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French (fr)
Japanese (ja)
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美伝 陳
正 藤枝
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株式会社日立製作所
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    • 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
    • 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
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
    • B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
    • 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
    • B33Y70/00—Materials specially adapted for 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese

Definitions

  • the present invention relates to an additive manufacturing powder, an additive manufacturing product, and a method of manufacturing an additive manufacturing product.
  • the metal powder additive manufacturing method has been drawing attention in recent years because it can produce parts with a desired shape in a near net shape. Research to solve various problems that occur during modeling continues to develop.
  • Patent Document 1 discloses an iron-based powder material used when forming an iron-based sintered body by irradiating a high-energy beam to partially or completely melt and solidify the iron-based powder material. Then, Si: 0.7 to 8.0%, S: 0.04 to 0.6%, C: 0.005 to 1%, Mn: 0.2 to 15%, P: 0.05% or less ( An iron-based powder material for forming an iron-based sintered body, the content of which is 0%). Patent Document 1 describes that it is possible to provide a powder material that can suppress the occurrence of cracks induced in a sintered body by rapid melting, rapid solidification, etc., and can improve the surface roughness that affects the shape accuracy.
  • Patent Document 2 a metal powder used for metal stereolithography to form a three-dimensional shape by stacking a sintered layer obtained by irradiating a metal powder material with a light beam is used.
  • Co is contained in an amount of 0 wt% or more and 4 wt% or less
  • Si is included in an amount of 0 wt% or more and 0.5 wt% or less
  • Mn is included in an amount of 0 wt% or more and 0.5 wt% or less
  • Cr+Ni is 16 wt% or more and 19 wt% or more.
  • a metal powder for metal stereolithography characterized in that the content of Cu+Ti+Co is 8% by weight or more and 9% by weight or less, and the amount of Si+Mn is 0% by weight or more and 1% by weight or less. According to Patent Document 2, it is described that it is possible to provide a metal powder for metal stereolithography, which can obtain a modeled article having excellent hardness, thermal conductivity, and corrosion resistance.
  • post-heat treatment is usually performed to control the structure in order to remove residual stress of the layered products, solid solution of elements, and precipitation strengthening.
  • the SUS316L modeled product has a columnar crystal structure along the modeling direction after modeling, and the mechanical properties are anisotropic.
  • post heat treatment is performed.
  • the material is sensitized during the post heat treatment, or the crystal grain size is coarsened to cause softening.
  • an object of the present invention is to eliminate the need for post heat treatment after layered modeling, and to obtain a layered model having strength equal to or higher than that of the conventional powder for layered modeling, a layered model, and a layered model. It is to provide a manufacturing method.
  • One aspect of the present invention for achieving the above object is characterized by including an iron-based alloy containing Ti in an amount of 0.1% by mass or more and 6% by mass or less and B in an amount of 0.2% by mass or more and 2% by mass or less. Is a powder for additive manufacturing.
  • Another embodiment of the present invention for achieving the above object is to have an iron-based alloy containing 0.1% by mass or more and 6% by mass or less of Ti and 0.2% by mass or more and 2% by mass or less of B, TiB and It is a layered structure characterized by having a crystal containing at least one of TiB 2 .
  • Another aspect of the present invention for achieving the above object is a raw material mixing and melting step of preparing a molten metal by mixing and melting raw materials of an iron-based alloy, and an atomizing step of producing a powder of the iron-based alloy from the molten metal. And a layered manufacturing/sintering step of manufacturing a layered body using the powder, wherein the powder contains 0.1% by mass or more and 6% by mass or less of Ti and 0.2% by mass or more and 2% by mass of B. % Or less, and in the additive manufacturing/sintering step, a crystal including at least one of TiB and TiB 2 is precipitated in the iron-based alloy.
  • Electron backscattering diffraction image showing the structure after laser irradiation simulating the additive manufacturing of Sample 1.
  • An electron backscattering diffraction image (A) showing an example of the structure of a layered product produced by overlaying SUS316L, and an electron rear showing an example of the structure of a layered product produced by overlaying Sample 2 Scattering diffraction method image (EBSD image) (B)
  • the present inventor in order to eliminate sensitization and softening by post-heat treatment of the iron-based alloy molded article, has a fine and non-anisotropic structure without post-heat treatment, and has higher mechanical properties.
  • the inventors have earnestly studied the development of the alloy material shown. As a result, a predetermined amount of Ti and B was added to the iron-based alloy, and at least one crystal of TiB or TiB 2 was finely dispersed in the layered structure to form an equiaxed crystal structure. , Found that the mechanical properties can be improved.
  • the present invention is based on this finding.
  • the powder for additive manufacturing of the present invention contains 0.1% by mass or more and 6% by mass or less of Ti (titanium) and 0.2% by mass or more and 2% by mass or less of B (boron) in the iron-based alloy.
  • Ti titanium
  • B boron
  • the layered model is usually subjected to post-heat treatment by heating the alloy to a recrystallization temperature or higher (for example, 1000° C. or higher in SUS316L) after modeling to eliminate crystal anisotropy (equix crystal).
  • a recrystallization temperature or higher for example, 1000° C. or higher in SUS316L
  • crystal anisotropy equix crystal
  • at least one of TiB and TiB 2 is deposited on the additive manufacturing body by having the composition described above.
  • This TiB or TiB 2 serves as a crystal nucleus for recrystallization, has the effect of pinning the movement of crystal grain boundaries at the same time as the structure is refined, and can suppress the growth of columnar crystals.
  • the Ti content is less than 0.1% by mass and the B content is less than 0.2% by mass, it is not sufficient to precipitate TiB or TiB 2 . If the Ti content exceeds 6 mass %, it is not preferable from the viewpoint of cost. B has a low melting point and rapidly solidifies. Therefore, if the content exceeds 2 mass %, cracking tends to occur after layered manufacturing, which is not preferable.
  • the total content of Ti and B is more preferably 1.5% by mass or more and 2% by mass or less.
  • the additive manufacturing powder preferably has an iron-based alloy composition, more specifically, an austenitic stainless steel composition. More specifically, C (carbon) is 0.08 mass% or less, Mn (manganese) is 2 mass% or less, Ni (nickel) is 10 mass% or more and 15 mass% or less, and Cr (chrome) is 16 mass%. A composition containing 18% by mass or more and 2% by mass or more and 3% by mass or less of Mo (molybdenum) with the balance being Fe (iron) and an unavoidable element is preferable.
  • One of alloys having such a composition is SUS316L.
  • FIG. 1 is a process drawing showing an example of the additive manufacturing powder, additive manufacturing object, and method for manufacturing additive manufacturing objects of the present invention.
  • the method for manufacturing a layered modeling body includes a raw material mixing and melting step (S1), an atomizing step (S2), and a layered modeling/sintering step (S3).
  • S1 to S3 will be described in detail.
  • raw materials are mixed and melted so as to have a desired alloy composition, and a molten metal 10 is produced.
  • the mixing method or the melting method of the raw materials there is no particular limitation on the mixing method or the melting method of the raw materials, and the conventional method in the production of the iron-based alloy can be used.
  • vacuum melting can be preferably used as the melting method.
  • the alloy composition is as described above.
  • the alloy powder 20 is formed from the molten metal 10.
  • the alloy powder 20 obtained in this step S2 is one form of the additive manufacturing powder of the present invention.
  • the conventional method can be used.
  • a gas atomizing method or a centrifugal atomizing method which can obtain spherical particles having a high purity, a homogeneous composition, can be preferably used.
  • the average particle size of the alloy powder 20 of the present invention is not particularly limited, but is preferably 5 ⁇ m or more and 200 ⁇ m or less, and 10 ⁇ m or more and 100 ⁇ m or less from the viewpoint of fluidity and filling property when molding using the alloy powder 20. More preferred is 10 ⁇ m or more and 50 ⁇ m or less.
  • the average particle size of the alloy powder 20 when the average particle size of the alloy powder 20 is less than 5 ⁇ m, the fluidity of the alloy powder 20 decreases (for example, the formability of the alloy powder bed in additive manufacturing decreases), This is a factor that reduces the shape accuracy of the modeled object.
  • the average particle size of the alloy powder 20 exceeds 200 ⁇ m, it becomes difficult to control the local melting and rapid solidification of the alloy powder bed in the layered modeling step S3, the melting of the alloy powder 20 becomes insufficient, and It becomes a factor of increasing roughness.
  • an alloy molded article (AM body) having a desired shape is formed by a additive manufacturing method (also referred to as an AM method) using the alloy powder 20 prepared above.
  • the AM body 30 obtained in this step S3 is one form of the layered modeling body of the present invention.
  • the additive manufacturing method is not particularly limited, and a conventional method can be used, but it is preferable to use, for example, a selective laser melting (SLM) method or a laser overlay.
  • SLM selective laser melting
  • the AM body 30 includes at least one crystal of TiB and TiB 2 . This was precipitated from the iron-based alloy in this step, and the crystal grain size is 100 ⁇ m or less. By finely dispersing TiB or TiB 2 crystals in the alloy structure after the additive manufacturing, an equiaxed crystal structure can be formed and mechanical properties can be improved. By having such a structure, it is possible to achieve strength equal to or higher than conventional strength without performing post heat treatment after layered manufacturing.
  • the AM body may be, for example, an impeller of a fluid machine (compressor, pump, etc.).
  • Example 1 (Laser irradiation test simulating additive manufacturing)
  • 0.1% by mass of Ti and 1.9% by mass of B were added to SUS316L alloy powder to prepare Sample 1 by casting.
  • the surface of Sample 1 was irradiated with a laser, and the structure of the cross section of the irradiated portion was observed.
  • FIG. 2 is an electron backscattering diffractometry image (EBSD image) showing the structure of the sample 1 after laser irradiation simulating the additive manufacturing. As shown in FIG. 2, fine and equiaxed crystal grains having an average grain size of 20 ⁇ m or less were observed in the center of Sample 1.
  • EBSD image electron backscattering diffractometry image
  • FIG. 3 is an electron backscattering diffraction image (EBSD image) (A) showing an example of the structure of a layered product produced by overlaying SUS316L, and an example of the structure of a layered product produced by overlaying Sample 2 It is an electron backscattering diffraction image (EBSD image) (B) shown. From FIG.
  • EBSD image electron backscattering diffraction image
  • SUS316L has a columnar crystal structure having an average crystal grain size of 100 ⁇ m or more along the build-up modeling method (longitudinal direction).
  • FIG. 3B it is confirmed that the sample 2 has a columnar crystal structure disappeared and a large number of fine crystals are generated as compared with SUS316L.
  • a tensile test piece with a brim is cut out from the overlay material of SUS316L and Sample 2 described above, and a dual column floor-standing tester (manufactured by Instron Co., model: Instron 5982) is used at room temperature in accordance with JIS Z2241. The yield strength and tensile strength were measured at. The tensile strength and yield strength of SUS316L and Sample 2 are shown in Table 1 described later.
  • Table 1 shows the yield strength and tensile strength after the post-heat treatment (1010 to 1150°C, rapid cooling) of SUS316L.
  • the yield strength and tensile strength of Sample 2 are much higher than those of SUS316L without post heat treatment. Further, even when compared with the value after the conventional post-heat treatment of SUS316L, the yield strength and the tensile strength of Sample 2 have reached the same or higher level.
  • the present invention is not limited to the above-described embodiments, and various modifications are included.
  • the above-described embodiments have been described in detail in order to explain the present invention in an easy-to-understand manner, and are not necessarily limited to those having all the configurations described.
  • a part of the configuration of one embodiment can be replaced with the configuration of another embodiment, and the configuration of another embodiment can be added to the configuration of one embodiment.

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  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
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Abstract

Provided are: a powder for laminate formation use, which enables the production of a laminated article having strength equivalent to or better than those of the conventional laminated articles without the need of a post-thermal treatment after laminate formation; a laminated article; and a method for producing a laminated article.　The powder for laminate formation use according to the present invention is characterized by comprising an iron-based alloy containing 0.1 to 6% by mass inclusive of Ti and 0.2 to 2% by mass inclusive of B.　The laminated article according to the present invention is characterized by comprising an iron-based alloy containing 0.1 to 6% by mass inclusive of Ti and 0.2 to 2% by mass inclusive of B and containing crystals each containing at least one of TiB and TiB2. The method for producing a laminated article according to the present invention is characterized by causing the precipitation of crystals each containing at least one of TiB and TiB2 in an iron-based alloy in a laminate-formation/sintering step using a powder for laminate formation use which comprises an iron-based alloy containing 0.1 to 6% by mass inclusive of Ti and 0.2 to 2% by mass inclusive of B.

Description

積層造形用粉末、積層造形体および積層造形体の製造方法Powder for additive manufacturing, additive manufacturing object, and method for producing additive object
　本発明は、積層造形用粉末、積層造形体および積層造形体の製造方法に関する。 The present invention relates to an additive manufacturing powder, an additive manufacturing product, and a method of manufacturing an additive manufacturing product.
　金属粉末積層造形法は、望ましい形状の部品をニアネットシェイプで作製することが可能であるため、近年注目が集まっている。造形時に生じるさまざまな課題を解決するための研究も発展し続けている。 The metal powder additive manufacturing method has been drawing attention in recent years because it can produce parts with a desired shape in a near net shape. Research to solve various problems that occur during modeling continues to develop.
　特許文献１には、高エネルギービームを照射して、鉄系粉末材料を部分的または完全に溶融凝固させて鉄基焼結体を形成する際に用いられる鉄系粉末材料であって、質量％で、Ｓｉ：０．７～８．０％、Ｓ：０．０４～０．６％、Ｃ：０．００５～１％、Ｍｎ：０．２～１５％、Ｐ：０．０５％以下（０％を含む）をそれぞれ含有することを特徴とする、鉄基焼結体形成用の鉄系粉末材料が開示されている。特許文献１には、急速溶融・急冷凝固等によって焼結体に誘起される割れの発生を抑制し、かつ形状精度に影響する表面粗度を改善できる粉末材料を提供できると記載されている。 Patent Document 1 discloses an iron-based powder material used when forming an iron-based sintered body by irradiating a high-energy beam to partially or completely melt and solidify the iron-based powder material. Then, Si: 0.7 to 8.0%, S: 0.04 to 0.6%, C: 0.005 to 1%, Mn: 0.2 to 15%, P: 0.05% or less ( An iron-based powder material for forming an iron-based sintered body, the content of which is 0%). Patent Document 1 describes that it is possible to provide a powder material that can suppress the occurrence of cracks induced in a sintered body by rapid melting, rapid solidification, etc., and can improve the surface roughness that affects the shape accuracy.
　また、特許文献２には、金属の粉末材料に光ビームを照射して得られる焼結層を積層することで、三次元形状を造形する金属光造形に用いる金属粉末であって、Ｆｅを７１重量％以上７６重量％以下、Ｃｒを１０重量％以上１３重量％以下、Ｎｉを４重量％以上９重量％以下、Ｃｕを４重量％以上７重量％以下、Ｔｉを２重量％以上３重量％以下、Ｃｏを０重量％以上４重量％以下、Ｓｉを０重量％以上０．５重量％以下、Ｍｎを０重量％以上０．５重量％以下を含有し、且つＣｒ＋Ｎｉが１６重量％以上１９重量％以下、Ｃｕ＋Ｔｉ＋Ｃｏが８重量％以上９重量％以下、Ｓｉ＋Ｍｎが０重量％以上１重量％以下であることを特徴とする金属光造形用金属粉末が開示されている。特許文献２によれば、硬度、熱伝導率、耐食性に優れた造形物を得ることができる金属光造形用金属粉末を提供することができると記載されている。 Further, in Patent Document 2, a metal powder used for metal stereolithography to form a three-dimensional shape by stacking a sintered layer obtained by irradiating a metal powder material with a light beam is used. Wt% to 76 wt%, Cr 10 wt% to 13 wt%, Ni 4 wt% to 9 wt%, Cu 4 wt% to 7 wt%, Ti 2 wt% to 3 wt% In the following, Co is contained in an amount of 0 wt% or more and 4 wt% or less, Si is included in an amount of 0 wt% or more and 0.5 wt% or less, Mn is included in an amount of 0 wt% or more and 0.5 wt% or less, and Cr+Ni is 16 wt% or more and 19 wt% or more. Disclosed is a metal powder for metal stereolithography, characterized in that the content of Cu+Ti+Co is 8% by weight or more and 9% by weight or less, and the amount of Si+Mn is 0% by weight or more and 1% by weight or less. According to Patent Document 2, it is described that it is possible to provide a metal powder for metal stereolithography, which can obtain a modeled article having excellent hardness, thermal conductivity, and corrosion resistance.
特開２００４－０７６０４０号公報Japanese Patent Laid-Open No. 2004-076040 特開２０１４－１０５３７３号公報JP, 2014-105373, A
　積層造形体の作製では、通常、積層造形物の残留応力除去、元素固溶および析出強化などを図るため、後熱処理を行って組織制御が行われている。たとえば、ＳＵＳ３１６Ｌ造形物は、造形後、造形方向に沿い柱状晶組織となり、機械的特性には異方性が生じる。それを解消するため（等軸晶に整える）に、後熱処理が行われる。一方、後熱処理する際に材料の鋭敏化が発生したり、結晶粒径が粗大化して軟化が起こったりすることが課題となることがある。 In the production of layered products, post-heat treatment is usually performed to control the structure in order to remove residual stress of the layered products, solid solution of elements, and precipitation strengthening. For example, the SUS316L modeled product has a columnar crystal structure along the modeling direction after modeling, and the mechanical properties are anisotropic. In order to eliminate it (to prepare equiaxed crystals), post heat treatment is performed. On the other hand, there may be a problem that the material is sensitized during the post heat treatment, or the crystal grain size is coarsened to cause softening.
　本発明の目的は、上記事情に鑑み、積層造形後の後熱処理を不要とし、従来と同等以上の強度を有する積層造形体を得ることができる積層造形用粉末、積層造形体および積層造形体の製造方法を提供することにある。 In view of the above circumstances, an object of the present invention is to eliminate the need for post heat treatment after layered modeling, and to obtain a layered model having strength equal to or higher than that of the conventional powder for layered modeling, a layered model, and a layered model. It is to provide a manufacturing method.
　上記目的を達成するための本発明の一態様は、Ｔｉを０．１質量％以上６質量％以下、Ｂを０．２質量％以上２質量％以下含有する鉄基合金を含むことを特徴とする積層造形用粉末である。 One aspect of the present invention for achieving the above object is characterized by including an iron-based alloy containing Ti in an amount of 0.1% by mass or more and 6% by mass or less and B in an amount of 0.2% by mass or more and 2% by mass or less. Is a powder for additive manufacturing.
　上記目的を達成するための本発明の他の態様は、Ｔｉを０．１質量％以上６質量％以下、Ｂを０．２質量％以上２質量％以下含む鉄基合金を有し、ＴｉＢおよびＴｉＢ２のうちの少なくとも１つを含む結晶を有することを特徴とする積層造形体である。 Another embodiment of the present invention for achieving the above object is to have an iron-based alloy containing 0.1% by mass or more and 6% by mass or less of Ti and 0.2% by mass or more and 2% by mass or less of B, TiB and It is a layered structure characterized by having a crystal containing at least one of TiB 2 .
　上記目的を達成するための本発明の他の態様は、鉄基合金の原料を混合・溶解して溶湯を作製する原料混合溶解工程と、溶湯から上記鉄基合金の粉末を作製するアトマイズ工程と、上記粉末を用いて積層造形体を作製する積層造形・焼結工程とを有し、上記粉末は、Ｔｉを０．１質量％以上６質量％以下、Ｂを０．２質量％以上２質量％以下含み、上記積層造形・焼結工程において、上記鉄基合金にＴｉＢおよびＴｉＢ２のうちの少なくとも１つを含む結晶を析出させることを特徴とする積層造形体の製造方法である。 Another aspect of the present invention for achieving the above object is a raw material mixing and melting step of preparing a molten metal by mixing and melting raw materials of an iron-based alloy, and an atomizing step of producing a powder of the iron-based alloy from the molten metal. And a layered manufacturing/sintering step of manufacturing a layered body using the powder, wherein the powder contains 0.1% by mass or more and 6% by mass or less of Ti and 0.2% by mass or more and 2% by mass of B. % Or less, and in the additive manufacturing/sintering step, a crystal including at least one of TiB and TiB 2 is precipitated in the iron-based alloy.
　本発明のより具体的な構成は、特許請求の範囲に記載される。 A more specific configuration of the present invention is described in the claims.
　積層造形後の後熱処理を不要とし、従来と同等以上の強度を有する積層造形体を得ることができる積層造形用粉末、積層造形体および積層造形体の製造方法を提供することができる。 It is possible to provide a powder for layered modeling, a layered model, and a method for manufacturing a layered model that do not require post-heat treatment after layered modeling and can obtain a layered model having strength equal to or higher than that of a conventional one.
　上記した以外の課題、構成および効果は、以下の実施形態の説明により明らかにされる。 Issues, configurations, and effects other than those described above will be clarified by the following description of the embodiments.
本発明の積層造形用粉末、積層造形体および積層造形体を製造する方法の一例を示す工程図Process drawing which shows an example of the method for manufacturing the powder for additive manufacturing, additive manufacturing object, and additive manufacturing object of the present invention 試料１の積層造形を模擬したレーザ照射後の組織を示す電子後方散乱回折法像（ＥＢＳＤ像）Electron backscattering diffraction image (EBSD image) showing the structure after laser irradiation simulating the additive manufacturing of Sample 1. ＳＵＳ３１６Ｌを肉盛によって作製した積層造形物の組織の一例を示す電子後方散乱回折法像（ＥＢＳＤ像）（Ａ）と、試料２を肉盛によって作製した積層造形物の組織の一例を示す電子後方散乱回折法像（ＥＢＳＤ像）（Ｂ）An electron backscattering diffraction image (EBSD image) (A) showing an example of the structure of a layered product produced by overlaying SUS316L, and an electron rear showing an example of the structure of a layered product produced by overlaying Sample 2 Scattering diffraction method image (EBSD image) (B)
　（本発明の基本思想）
　本発明者は、鉄基合金の造形物の後熱処理による鋭敏化、軟化を解消するため、後熱処理無しで、微細で、かつ、異方性の無い組織を有し、さらに高い機械的特性を示す合金材の開発について鋭意検討を行った。その結果、鉄基合金にＴｉおよびＢを所定量添加し、積層造形体にＴｉＢまたはＴｉＢ２のうちの少なくとも１つの結晶を合金組織中に微細に分散することにより、等軸晶組織を形成し、機械的特性を向上できることを見出した。本発明は、該知見に基づくものである。 (Basic idea of the present invention)
The present inventor, in order to eliminate sensitization and softening by post-heat treatment of the iron-based alloy molded article, has a fine and non-anisotropic structure without post-heat treatment, and has higher mechanical properties. The inventors have earnestly studied the development of the alloy material shown. As a result, a predetermined amount of Ti and B was added to the iron-based alloy, and at least one crystal of TiB or TiB 2 was finely dispersed in the layered structure to form an equiaxed crystal structure. , Found that the mechanical properties can be improved. The present invention is based on this finding.
　以下、本発明の実施形態について、図面を参照しながら詳細に説明する。ただし、本発明は、ここで取り挙げた実施形態に限定されるものではなく、発明の技術的思想を逸脱しない範囲で、公知技術と適宜組み合わせたり公知技術に基づいて改良したりすることが可能である。 Hereinafter, embodiments of the present invention will be described in detail with reference to the drawings. However, the present invention is not limited to the embodiments described here, and may be appropriately combined with or improved on the basis of a known technique without departing from the technical idea of the invention. Is.
　［積層造形用粉末］
　上述した通り、本発明の積層造形用粉末は、鉄基合金にＴｉ（チタン）を０．１質量％以上６質量％以下、Ｂ（ホウ素）を０．２質量％以上２質量％以下含む。このような組成を有することによって、固溶強化により強度を向上させると同時に、積層造形後の組織中に微細なＴｉＢおよびＴｉＢ２のうちの少なくとも１つを分散させることができる。 [Powder for additive manufacturing]
As described above, the powder for additive manufacturing of the present invention contains 0.1% by mass or more and 6% by mass or less of Ti (titanium) and 0.2% by mass or more and 2% by mass or less of B (boron) in the iron-based alloy. By having such a composition, strength can be improved by solid solution strengthening, and at the same time, at least one of fine TiB and TiB 2 can be dispersed in the structure after the additive manufacturing.
　積層造形体は、通常、造形後に合金を再結晶温度以上（例えば、ＳＵＳ３１６Ｌでは、１０００℃以上）に加熱し、結晶異方性を無くす（等軸晶）にする後熱処理が行われる。本発明の積層造形用は、上述した組成を有することによって積層造形体にＴｉＢおよびＴｉＢ２のうちの少なくとも１つを析出させる。このＴｉＢまたはＴｉＢ２が再結晶の結晶核となり、組織微細化と同時に結晶粒界の移動をピン止めする効果を発揮し、柱状晶の成長を抑制できる。この結果、積層造形後の後熱処理を行わなくても、結晶異方性を解消し、従来と同等以上の強度を達成することができる。 The layered model is usually subjected to post-heat treatment by heating the alloy to a recrystallization temperature or higher (for example, 1000° C. or higher in SUS316L) after modeling to eliminate crystal anisotropy (equix crystal). In the additive manufacturing of the present invention, at least one of TiB and TiB 2 is deposited on the additive manufacturing body by having the composition described above. This TiB or TiB 2 serves as a crystal nucleus for recrystallization, has the effect of pinning the movement of crystal grain boundaries at the same time as the structure is refined, and can suppress the growth of columnar crystals. As a result, it is possible to eliminate the crystal anisotropy and achieve a strength equal to or higher than that of the conventional one without performing post-heat treatment after the additive manufacturing.
　Ｔｉの含有量が０．１質量％未満およびＢの含有量が０．２質量％未満であると、ＴｉＢまたはＴｉＢ２を析出させるのに十分ではない。Ｔｉの含有量が６質量％を超えるとコストの観点で好ましくない。Ｂは融点が低く、凝固が早いため、含有量が２質量％を超えると、積層造形後の割れが生じやすくなり、好ましくない。 When the Ti content is less than 0.1% by mass and the B content is less than 0.2% by mass, it is not sufficient to precipitate TiB or TiB 2 . If the Ti content exceeds 6 mass %, it is not preferable from the viewpoint of cost. B has a low melting point and rapidly solidifies. Therefore, if the content exceeds 2 mass %, cracking tends to occur after layered manufacturing, which is not preferable.
　ＴｉとＢの合計含有量は、１．５質量％以上２質量％以下であることがより好ましい。 The total content of Ti and B is more preferably 1.5% by mass or more and 2% by mass or less.
　積層造形用粉末は、鉄基合金組成を有することが好ましく、より具体的にはオーステナイト系ステンレス鋼の組成であることが好ましい。さらに具体的には、Ｃ（炭素）を０．０８質量％以下、Ｍｎ（マンガン）を２質量％以下、Ｎｉ（ニッケル）を１０質量％以上１５質量％以下、Ｃｒ（クロム）を１６質量％以上１８質量％以下、Ｍｏ（モリブデン）を２質量％以上３質量％以下含み、残部がＦｅ（鉄）および不可避元素である組成が好ましい。このような組成を有する合金の１つとして、ＳＵＳ３１６Ｌが挙げられる。 The additive manufacturing powder preferably has an iron-based alloy composition, more specifically, an austenitic stainless steel composition. More specifically, C (carbon) is 0.08 mass% or less, Mn (manganese) is 2 mass% or less, Ni (nickel) is 10 mass% or more and 15 mass% or less, and Cr (chrome) is 16 mass%. A composition containing 18% by mass or more and 2% by mass or more and 3% by mass or less of Mo (molybdenum) with the balance being Fe (iron) and an unavoidable element is preferable. One of alloys having such a composition is SUS316L.
　［積層造形体］
　次に、上述した本発明の積層造形用鉄基合金粉末を用いて作製した鉄基積層造形体について、その製造方法に沿って説明する。図１は本発明の積層造形用粉末、積層造形体および積層造形体を製造する方法の一例を示す工程図である。図１に示すように、積層造形体の製造方法は、原料混合溶解工程（Ｓ１）と、アトマイズ工程（Ｓ２）と、積層造形・焼結工程（Ｓ３）を有する。以下にＳ１～Ｓ３について詳述する。 [Layered object]
Next, an iron-based layered modeling product produced using the above-described iron-based alloy powder for layered modeling of the present invention will be described along with its manufacturing method. FIG. 1 is a process drawing showing an example of the additive manufacturing powder, additive manufacturing object, and method for manufacturing additive manufacturing objects of the present invention. As shown in FIG. 1, the method for manufacturing a layered modeling body includes a raw material mixing and melting step (S1), an atomizing step (S2), and a layered modeling/sintering step (S3). Hereinafter, S1 to S3 will be described in detail.
　Ｓ１：原料混合溶解工程
　原料混合溶解工程Ｓ１では、所望の合金組成となるように原料を混合・溶解して溶湯１０を作製する。原料の混合方法や溶解方法に特段の限定はなく、鉄基合金の製造における従前の方法を利用できる。例えば、溶解方法として真空溶解を好適に利用できる。また、真空炭素脱酸法などを併用して、溶湯１０を精錬することが好ましい。合金組成は、上述した通りである。 S1: Raw Material Mixing and Melting Step In the raw material mixing and melting step S1, raw materials are mixed and melted so as to have a desired alloy composition, and a molten metal 10 is produced. There is no particular limitation on the mixing method or the melting method of the raw materials, and the conventional method in the production of the iron-based alloy can be used. For example, vacuum melting can be preferably used as the melting method. Further, it is preferable to refine the molten metal 10 by using a vacuum carbon deoxidizing method in combination. The alloy composition is as described above.
　Ｓ２：アトマイズ工程
　アトマイズ工程Ｓ２では、溶湯１０から合金粉末２０を形成する。本工程Ｓ２で得られる合金粉末２０が、本発明の積層造形用粉末の一形態である。アトマイズ方法に特段の限定はなく、従前の方法を利用できる。例えば、高純度・均質組成・球形状粒子が得られるガスアトマイズ法や遠心力アトマイズ法を好ましく用いることができる。 S2: Atomizing Step In the atomizing step S2, the alloy powder 20 is formed from the molten metal 10. The alloy powder 20 obtained in this step S2 is one form of the additive manufacturing powder of the present invention. There is no particular limitation on the atomizing method, and the conventional method can be used. For example, a gas atomizing method or a centrifugal atomizing method, which can obtain spherical particles having a high purity, a homogeneous composition, can be preferably used.
　本発明の合金粉末２０の平均粒径に特段の限定はないが、該合金粉末２０を用いて造形する際の流動性や充填性の観点から、５μｍ以上２００μｍ以下が好ましく、１０μｍ以上１００μｍ以下がより好ましく、１０μｍ以上５０μｍ以下が更に好ましい。 The average particle size of the alloy powder 20 of the present invention is not particularly limited, but is preferably 5 μm or more and 200 μm or less, and 10 μm or more and 100 μm or less from the viewpoint of fluidity and filling property when molding using the alloy powder 20. More preferred is 10 μm or more and 50 μm or less.
　後述する積層造形工程Ｓ３においては、合金粉末２０の平均粒径が５μｍ未満になると、合金粉末２０の流動性が低下して（例えば、積層造形における合金粉末床の形成性が低下して）、造形物の形状精度が低下する要因となる。一方、合金粉末２０の平均粒径が２００μｍ超になると、積層造形工程Ｓ３における合金粉末床の局所溶融・急冷凝固の制御が難しくなり、合金粉末２０の溶融が不十分になったり造形物の表面粗さが増加したりする要因となる。 In the additive manufacturing step S3 described below, when the average particle size of the alloy powder 20 is less than 5 μm, the fluidity of the alloy powder 20 decreases (for example, the formability of the alloy powder bed in additive manufacturing decreases), This is a factor that reduces the shape accuracy of the modeled object. On the other hand, if the average particle size of the alloy powder 20 exceeds 200 μm, it becomes difficult to control the local melting and rapid solidification of the alloy powder bed in the layered modeling step S3, the melting of the alloy powder 20 becomes insufficient, and It becomes a factor of increasing roughness.
　Ｓ３：積層造形・焼結工程
　積層造形工程Ｓ３では、上記で用意した合金粉末２０を用いた積層造形法（Ａｄｄｉｔｉｖｅ　Ｍａｎｕｆａｃｔｕｒｉｎｇ、ＡＭ法とも称する。）により、所望形状を有する合金造形物（ＡＭ体）３０を形成する。本工程Ｓ３で得られるＡＭ体３０が、本発明の積層造形体の一形態である。焼成炉による焼結ではなく、レーザによる局所溶融・急冷凝固によってニアネットシェイプの金属部材を造形する積層造形法の適用により、鍛造材と同等以上の硬度とともに、複雑形状を有する三次元部材を作製することができる。積層造形方法に特段の限定はなく、従前の方法を利用できるが、例えば、選択的レーザ溶融（ＳＬＭ）法、レーザ肉盛を用いることが好ましい。 S3: Additive Manufacturing/Sintering Step In the additive manufacturing step S3, an alloy molded article (AM body) having a desired shape is formed by a additive manufacturing method (also referred to as an AM method) using the alloy powder 20 prepared above. Form 30. The AM body 30 obtained in this step S3 is one form of the layered modeling body of the present invention. By applying the additive manufacturing method to form a near net shape metal member by local melting and rapid solidification by laser instead of sintering in a firing furnace, a three-dimensional member with a complicated shape with hardness equal to or higher than that of a forged material is applied. can do. The additive manufacturing method is not particularly limited, and a conventional method can be used, but it is preferable to use, for example, a selective laser melting (SLM) method or a laser overlay.
　ＡＭ体３０は、上述した通り、ＴｉＢおよびＴｉＢ２のうちの少なくとも１つの結晶を含む。これは、本工程において鉄基合金から析出したものであり、この結晶の粒径は、１００μｍ以下である。積層造形後にＴｉＢまたはＴｉＢ２の結晶を合金組織中に微細に分散することにより、等軸晶組織を形成し、機械的特性を向上できる。このような組織を有することによって、積層造形後に後熱処理を行うこと無く、従来と同等以上の強度を達成することができる。 As described above, the AM body 30 includes at least one crystal of TiB and TiB 2 . This was precipitated from the iron-based alloy in this step, and the crystal grain size is 100 μm or less. By finely dispersing TiB or TiB 2 crystals in the alloy structure after the additive manufacturing, an equiaxed crystal structure can be formed and mechanical properties can be improved. By having such a structure, it is possible to achieve strength equal to or higher than conventional strength without performing post heat treatment after layered manufacturing.
　ＡＭ体としては、例えば流体機械（圧縮機およびポンプ等）のインペラが挙げられる。 The AM body may be, for example, an impeller of a fluid machine (compressor, pump, etc.).
　以下、実施例に基づき、本発明についてより詳細に説明する。 Hereinafter, the present invention will be described in more detail based on examples.
　（積層造形を模擬したレーザ照射試験）
　実施例１では、ＳＵＳ３１６Ｌ合金粉末にＴｉを０．１質量％およびＢを１．９質量％添加した試料１を鋳造により作製した。積層造形を模擬した試験として、試料１の表面にレーザを照射し、照射部分の断面の組織観察を行った。図２は試料１の積層造形を模擬したレーザ照射後の組織を示す電子後方散乱回折法像（ＥＢＳＤ像）である。図２に示すように、試料１の中心部に平均粒径２０μｍ以下の微細かつ等軸の結晶粒が観察された。 (Laser irradiation test simulating additive manufacturing)
In Example 1, 0.1% by mass of Ti and 1.9% by mass of B were added to SUS316L alloy powder to prepare Sample 1 by casting. As a test simulating additive manufacturing, the surface of Sample 1 was irradiated with a laser, and the structure of the cross section of the irradiated portion was observed. FIG. 2 is an electron backscattering diffractometry image (EBSD image) showing the structure of the sample 1 after laser irradiation simulating the additive manufacturing. As shown in FIG. 2, fine and equiaxed crystal grains having an average grain size of 20 μm or less were observed in the center of Sample 1.
　（レーザ肉盛による積層造形物の微細組織観察および強度評価）
　実施例２では、ＳＵＳ３１６Ｌ合金粉末にＴｉを０．５質量％およびＢを１．５質量％添加した試料２の粉末を用い、レーザ肉盛試験を行った。作製した試料２の断面の組織観察を行った。図３はＳＵＳ３１６Ｌを肉盛による作製した積層造形物の組織の一例を示す電子後方散乱回折法像（ＥＢＳＤ像）（Ａ）と、試料２を肉盛によって作製した積層造形物の組織の一例を示す電子後方散乱回折法像（ＥＢＳＤ像）（Ｂ）である。図３の（Ａ）から、ＳＵＳ３１６Ｌは肉盛の造形方（縦方向）に沿い、平均結晶粒径１００μｍ以上の柱状晶組織になっている。一方、図３の（Ｂ）に示すように、試料２はＳＵＳ３１６Ｌに比べ、柱状晶組織が消え、微細な結晶が多数生成していることが確認される。 (Microstructural observation and strength evaluation of layered product by laser overlay)
In Example 2, the laser build-up test was performed using the powder of Sample 2 in which 0.5 mass% of Ti and 1.5 mass% of B were added to the SUS316L alloy powder. The structure of the cross section of the prepared sample 2 was observed. FIG. 3 is an electron backscattering diffraction image (EBSD image) (A) showing an example of the structure of a layered product produced by overlaying SUS316L, and an example of the structure of a layered product produced by overlaying Sample 2 It is an electron backscattering diffraction image (EBSD image) (B) shown. From FIG. 3A, SUS316L has a columnar crystal structure having an average crystal grain size of 100 μm or more along the build-up modeling method (longitudinal direction). On the other hand, as shown in FIG. 3B, it is confirmed that the sample 2 has a columnar crystal structure disappeared and a large number of fine crystals are generated as compared with SUS316L.
　上述したＳＵＳ３１６Ｌおよび試料２の肉盛材から、つば付形状の引張試験片を切り出し、デュアルコラム床置型試験機（インストロン社製、型式：Ｉｎｓｔｒｏｎ　５９８２）を用い、ＪＩＳ　Ｚ　２２４１に準拠して室温において降伏強さおよび引張強さを測定した。ＳＵＳ３１６Ｌおよび試料２の引張強さおよび降伏強さを後述する表１に示す。 A tensile test piece with a brim is cut out from the overlay material of SUS316L and Sample 2 described above, and a dual column floor-standing tester (manufactured by Instron Co., model: Instron 5982) is used at room temperature in accordance with JIS Z2241. The yield strength and tensile strength were measured at. The tensile strength and yield strength of SUS316L and Sample 2 are shown in Table 1 described later.
　また、ＳＵＳ３１６Ｌの後熱処理（１０１０～１１５０℃、急冷）後の降伏強さおよび引張強さを表１に併記する。 Also, Table 1 shows the yield strength and tensile strength after the post-heat treatment (1010 to 1150°C, rapid cooling) of SUS316L.
Figure JPOXMLDOC01-appb-T000001
Figure JPOXMLDOC01-appb-T000001
　表１に示すように、試料２の降伏強さおよび引張強さは、後熱処理なしのＳＵＳ３１６Ｌに比べてはるかに高い値となっている。また、従来のＳＵＳ３１６Ｌの後熱処理後の値と比較しても、試料２の降伏強さおよび引張強さは同等以上のレベルを達成している。 As shown in Table 1, the yield strength and tensile strength of Sample 2 are much higher than those of SUS316L without post heat treatment. Further, even when compared with the value after the conventional post-heat treatment of SUS316L, the yield strength and the tensile strength of Sample 2 have reached the same or higher level.
　以上、説明したように、本発明によれば、積層造形後の後熱処理を不要とし、従来と同等以上の強度を有する造形体を得ることができる積層造形用粉末および積層造形体を提供できることが実証された。 As described above, according to the present invention, it is possible to provide a layered modeling powder and a layered modeling body that do not require post heat treatment after layered modeling and that can obtain a modeled body having a strength equal to or higher than that of a conventional one. It was proven.
　なお、本発明は上記した実施例に限定されるものではなく、様々な変形例が含まれる。例えば、上記した実施例は本発明を分かり易く説明するために詳細に説明したものであり、必ずしも説明した全ての構成を備えるものに限定されるものではない。また、ある実施例の構成の一部を他の実施例の構成に置き換えることが可能であり、ある実施例の構成に他の実施例の構成を加えることも可能である。また、各実施例の構成の一部について、他の構成の追加や削除または置換をすることが可能である。 It should be noted that the present invention is not limited to the above-described embodiments, and various modifications are included. For example, the above-described embodiments have been described in detail in order to explain the present invention in an easy-to-understand manner, and are not necessarily limited to those having all the configurations described. Further, a part of the configuration of one embodiment can be replaced with the configuration of another embodiment, and the configuration of another embodiment can be added to the configuration of one embodiment. Further, it is possible to add, delete, or replace a part of the configuration of each embodiment with another configuration.
　１０…溶湯、２０…合金粉末、３０…合金造形物。 10... molten metal, 20... alloy powder, 30... alloy shaped article.

Claims (10)

  1. 　Ｔｉを０．１質量％以上６質量％以下、Ｂを０．２質量％以上２質量％以下含む鉄基合金を有することを特徴とする積層造形用粉末。 Additive-forming powder characterized by having an iron-based alloy containing 0.1% by mass to 6% by mass of Ti and 0.2% by mass to 2% by mass of B.
  2. 　前記鉄基合金は、さらに、Ｃを０．０８質量％以下、Ｍｎを２質量％以下、Ｎｉを１０質量％以上１５質量％以下、Ｃｒを１６質量％以上１８質量％以下、Ｍｏを２質量％以上３質量％以下含み、残部が鉄および不可避元素であることを特徴とする請求項１に記載の積層造形用粉末。 The iron-based alloy further contains 0.08 mass% or less of C, 2 mass% or less of Mn, 10 mass% or more and 15 mass% or less of Ni, 16 mass% or more and 18 mass% or less of Cr, and 2 mass% of Mo. % Or more and 3 mass% or less, and the balance is iron and unavoidable elements, The additive manufacturing powder according to claim 1.
  3. 　前記積層造形用粉末の平均粒径が５μｍ以上２００μｍ以下であることを特徴とする請求項１または２に記載の積層造形用粉末。 The additive manufacturing powder according to claim 1 or 2, wherein the additive manufacturing powder has an average particle size of 5 µm or more and 200 µm or less.
  4. 　Ｔｉを０．１質量％以上６質量％以下、Ｂを０．２質量％以上２質量％以下含む鉄基合金を有し、
    　ＴｉＢおよびＴｉＢ２のうちの少なくとも１つを含む結晶を有することを特徴とする積層造形体。     An iron-based alloy containing Ti in an amount of 0.1% by mass or more and 6% by mass or less and B in an amount of 0.2% by mass or more and 2% by mass or less,
    A layered product, comprising a crystal containing at least one of TiB and TiB 2 .
  5. 　前記結晶は、前記鉄基合金の析出物であることを特徴とする請求項４に記載の積層造形体。 The layered product according to claim 4, wherein the crystal is a precipitate of the iron-based alloy.
  6. 　前記鉄基合金は、さらに、Ｃを０．０８質量％以下、Ｍｎを２質量％以下、Ｎｉを１０質量％以上１５質量％以下、Ｃｒを１６質量％以上１８質量％以下、Ｍｏを２質量％以上３質量％以下含み、残部が鉄および不可避元素であることを特徴とする請求項４に記載の積層造形体。 The iron-based alloy further contains 0.08 mass% or less of C, 2 mass% or less of Mn, 10 mass% or more and 15 mass% or less of Ni, 16 mass% or more and 18 mass% or less of Cr, and 2 mass% of Mo. % Or more and 3 mass% or less, and the balance is iron and unavoidable elements, The layered product according to claim 4.
  7. 　前記積層造形体が、流体機械のインペラであることを特徴とする請求項４～６のいすれか１項に記載の積層造形体。 The layered product according to any one of claims 4 to 6, wherein the layered product is an impeller of a fluid machine.
  8. 　鉄基合金の原料を混合・溶解して溶湯を作製する原料混合溶解工程と、
    　前記溶湯から前記鉄基合金の粉末を作製するアトマイズ工程と、
    　前記粉末を用いて積層造形体を作製する積層造形・焼結工程とを有し、
    　前記粉末は、Ｔｉを０．１質量％以上６質量％以下、Ｂを０．２質量％以上２質量％以下含み、
    　前記積層造形・焼結工程において、前記鉄基合金にＴｉＢおよびＴｉＢ２のうちの少なくとも１つを含む結晶を析出させることを特徴とする積層造形体の製造方法。     A raw material mixing and melting step of mixing and melting the raw materials of the iron-based alloy to produce a molten metal;
    An atomizing step of producing powder of the iron-based alloy from the molten metal,
    And a layered manufacturing/sintering step of manufacturing a layered molded body using the powder,
    The powder contains 0.1% by mass or more and 6% by mass or less of Ti and 0.2% by mass or more and 2% by mass or less of B,
    A method for producing a layered body, wherein in the layered body forming/sintering step, crystals containing at least one of TiB and TiB 2 are precipitated in the iron-based alloy.
  9. 　前記鉄基合金は、さらに、Ｃを０．０８質量％以下、Ｍｎを２質量％以下、Ｎｉを１０質量％以上１５質量％以下、Ｃｒを１６質量％以上１８質量％以下、Ｍｏを２質量％以上３質量％以下含み、残部が鉄および不可避元素であることを特徴とする請求項８に記載の積層造形体の製造方法。 The iron-based alloy further contains 0.08 mass% or less of C, 2 mass% or less of Mn, 10 mass% or more and 15 mass% or less of Ni, 16 mass% or more and 18 mass% or less of Cr, and 2 mass% of Mo. % Or more and 3 mass% or less, and the balance is iron and an unavoidable element, The manufacturing method of the layered-molding body of Claim 8 characterized by the above-mentioned.
  10. 　前記粉末の平均粒径が５μｍ以上２００μｍ以下であることを特徴とする請求項８または９に記載の積層造形体の製造方法。 The method for producing a layered product according to claim 8 or 9, characterized in that the average particle size of the powder is 5 µm or more and 200 µm or less.
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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN115725908A (en) * 2021-08-27 2023-03-03 丰田自动车株式会社 High-rigidity iron-based alloy and method for producing same
WO2023157425A1 (en) 2022-02-17 2023-08-24 Ｊｆｅスチール株式会社 Stainless steel powder, stainless steel member, and stainless steel member manufacturing method

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5623256A (en) * 1979-07-31 1981-03-05 Daido Steel Co Ltd Composite material
JPH08100243A (en) * 1994-08-05 1996-04-16 Toyota Motor Corp Highly heat resistant iron-bas alloy
JP2014105373A (en) * 2012-11-29 2014-06-09 Canon Inc Metal powder for metal photofabrication, method of manufacturing molding die for injection molding, and molded article
JP2018172739A (en) * 2017-03-31 2018-11-08 株式会社フジミインコーポレーテッド Mold material for use in powder laminate molding

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5623256A (en) * 1979-07-31 1981-03-05 Daido Steel Co Ltd Composite material
JPH08100243A (en) * 1994-08-05 1996-04-16 Toyota Motor Corp Highly heat resistant iron-bas alloy
JP2014105373A (en) * 2012-11-29 2014-06-09 Canon Inc Metal powder for metal photofabrication, method of manufacturing molding die for injection molding, and molded article
JP2018172739A (en) * 2017-03-31 2018-11-08 株式会社フジミインコーポレーテッド Mold material for use in powder laminate molding

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN115725908A (en) * 2021-08-27 2023-03-03 丰田自动车株式会社 High-rigidity iron-based alloy and method for producing same
CN115725908B (en) * 2021-08-27 2024-06-07 丰田自动车株式会社 High-rigidity iron-based alloy and method for producing same
WO2023157425A1 (en) 2022-02-17 2023-08-24 Ｊｆｅスチール株式会社 Stainless steel powder, stainless steel member, and stainless steel member manufacturing method

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