WO2010024159A1 - Powder of tungsten alloy with transition metal dissolved therein as solid solution and process for producing same - Google Patents

Powder of tungsten alloy with transition metal dissolved therein as solid solution and process for producing same Download PDF

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WO2010024159A1
WO2010024159A1 PCT/JP2009/064494 JP2009064494W WO2010024159A1 WO 2010024159 A1 WO2010024159 A1 WO 2010024159A1 JP 2009064494 W JP2009064494 W JP 2009064494W WO 2010024159 A1 WO2010024159 A1 WO 2010024159A1
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tungsten
transition metal
solid solution
alloy powder
cobalt
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PCT/JP2009/064494
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French (fr)
Japanese (ja)
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政夫 森下
宏明 山本
政昭 池邉
政弘 岩崎
秀文 柳田
宏 西牧
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サンアロイ工業株式会社
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Priority to EP09809812A priority Critical patent/EP2332675A1/en
Priority to US12/737,875 priority patent/US20110243787A1/en
Priority to CN2009801335673A priority patent/CN102131601A/en
Publication of WO2010024159A1 publication Critical patent/WO2010024159A1/en

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/045—Alloys based on refractory metals
    • 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
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • 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
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps

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  • the present invention relates to a transition metal solid solution tungsten alloy powder and a method for producing the same.
  • Tungsten has a high melting point and elastic modulus, and is useful as a raw material for filament materials and tungsten carbide (WC).
  • WC tungsten carbide
  • the resources are mainly unevenly distributed in China, the price tends to rise with the rapid increase in domestic demand in China.
  • Patent Document 1 a method for producing a tungsten alloy powder by using a coprecipitation method of a metal salt or a metal hydroxide is conventionally known (Patent Document 1, Patent Document 2).
  • the alloy powder contains a transition metal element phase in addition to the tungsten phase and the tungsten phase alloyed with the transition metal element. Was not progressing sufficiently.
  • an object of the present invention is to provide a novel tungsten alloy powder in which a transition metal element is dissolved (including forced solid solution) and a method for producing the same.
  • the present inventor has conducted extensive research, and as a result, the tungsten ion and the transition metal ion are uniformly and uniformly formed in an aqueous solution at the ionic level, and after evaporating to dryness or spray drying, thermal decomposition is performed.
  • the inventors have found that when a tungsten powder is obtained by performing hydrogen thermal reduction, a tungsten alloy powder in which the transition metal element is completely forcibly dissolved can be produced, and the present invention is made here.
  • At least one transition metal element selected from the group consisting of cobalt, iron, manganese and nickel is dissolved in a tungsten lattice, and the formula [1 In the transition metal solid solution tungsten alloy powder.
  • M represents one or more selected from Co, Fe, Mn or Ni
  • transition metal solid solution tungsten alloy powder represented by the formula: Fe-W
  • Nickel is dissolved in tungsten lattice, formula: Ni-W
  • the transition metal solid solution tungsten alloy powder shown by these is mentioned.
  • a part of the cobalt, iron, and nickel can be substituted with one or more selected from the group of iron, manganese, and nickel, which are other transition metals, and a composite transition metal solid solution tungsten powder can be obtained.
  • the amount of transition metal dissolved in tungsten can be up to the equivalent mole of tungsten.
  • the second object of the present invention is to provide a production method for obtaining the transition metal solid solution tungsten powder, which is selected from the group consisting of an aqueous solution containing tungsten ions and cobalt, iron, iron-manganese and nickel.
  • An aqueous solution containing at least one kind of transition metal ions was mixed at a ratio of 60 mol% or more of tungsten ions and 40 mol% or less of transition metal ions, and the mixed aqueous solution was evaporated to dryness or spray dried.
  • MW where M is Co, One or more selected from Fe, Mn or Ni
  • the aqueous solution containing tungsten ions is an aqueous solution of ammonium paratungstate (5 (NH 4) 2 O ⁇ 12WO 3 ⁇ 5H 2 O), which is at least one selected from the group consisting of cobalt, iron, manganese and nickel.
  • the aqueous solution containing transition metal ions is preferably a transition metal complex salt aqueous solution.
  • transition metal complex salts As transition metal complex salts, acetate (Fe (OH) (C 2 H 3 OO) 2 , Co (C 2 H 3 O 3 ) 2 .4H 2 O, Mn (CH 3 COO) 2 .4H 2 O, Ni ( C 2 H 3 O 3 ) 2 ⁇ xH 2 O) and sulfates (FeSO 4 ⁇ 7H 2 O, CoSO 4 ⁇ 7H 2 O, NiSO 4 ⁇ 6H 2 O, MnSO 4 ⁇ 5H 2 O) it can.
  • sulfates FeSO 4 ⁇ 7H 2 O, CoSO 4 ⁇ 7H 2 O, NiSO 4 ⁇ 6H 2 O, MnSO 4 ⁇ 5H 2 O
  • the tungsten alloy powder obtained by the present invention is characterized in that the transition metal element is dissolved in the tungsten lattice and the bcc phase peak is observed in the X-ray diffraction pattern. Then, it turns out that a transition metal element or its metal compound does not exist substantially in a tungsten grain boundary.
  • the transition metal solid solution tungsten alloy powder represented by the formula [1] Formula [1]: MW (where M is Co, Fe, Mn or Ni) One or more selected)
  • the cobalt is basically contained in an amount of 0.3 to 20.8% by weight and the balance is made of tungsten, but all or a part of cobalt is replaced with one or more elements of iron, manganese and nickel. Is formed.
  • the M component including cobalt is less than 0.3% by weight of the tungsten alloy powder, the resource saving effect cannot be obtained, and if it exceeds 20.8% by weight, the second phase is precipitated at the tank stainless grain boundary, It can be seen that the tungsten alloy powder does not become a solid solution (forced solid solution) of the transition metal element.
  • Cobalt is present in substitution for the lattice position of tungsten, so that it acts as an alternative element for tungsten and is effective for resource saving of tungsten, which is rising in price.
  • catalytic activity can be increased by dissolving cobalt in a solid solution (forced solid solution), and the alloy powder of the present invention can be given a function as a catalyst.
  • nickel has a function similar to that of cobalt and is characterized by a lower price than cobalt. Nickel also imparts catalytic activity over cobalt.
  • Iron is characterized by improving the strength of tank stainless powder and being inexpensive.
  • iron and iron-manganese can effectively utilize their transformation characteristics, and can be used to improve the fracture toughness of the cemented carbide mold.
  • transition metal ions examples include metal complex salts such as iron, nickel, manganese and cobalt acetates (Co (C 2 H 3 O 3 ) 2 .4H 2 O, Fe (OH) (C 2 H 3 OO) 2 , Mn (CH 3 COO) 2 .4H 2 O, Ni (C 2 H 3 O 3 ) 2 .xH 2 O) are water-soluble and do not generate harmful substances. The load is small.
  • transition metal sulfates of iron, nickel and cobalt is also effective for realizing a recycling society.
  • copper electrorefining processes concentrate iron, nickel and cobalt transition metals in sulfuric acid in the electrolyte. Therefore, the waste liquid generated by electrolytic refining of copper can be used as a raw material for the tungsten alloy powder of the present invention, and sulfuric acid generated during evaporation to dryness or spray drying can also be effectively used as a by-product. .
  • tungsten metal complex salts may be used alone or in combination of two or more to form tungsten metal or It will be apparent to those skilled in the art from the examples that two or more transition metals can be dissolved and replaced with part of the tungsten metal.
  • the solution method is the process of the present invention, and includes transition metal acetates (Co (C 2 H 3 O 3 ) 2 .4H 2 O, Fe (OH) (C 2 H 3 OO) 2 , Mn
  • NH 4 ammonium paratungstate
  • Sample No. 1 is a powder metallurgy, which is a conventional technique of powder metallurgy, and 7.42% by weight of pure cobalt powder and the remaining pure tungsten powder are weighed and mixed to obtain the chemical composition shown in Table 1, and then 2 ton / cm.
  • This is a conventional material obtained by compression molding at a pressure of 2 and holding in hydrogen gas at 1073 K for 1 h. A pure cobalt phase remained as the second phase, and alloying with tungsten did not proceed.
  • Sample No. 2 is the material of the present invention obtained by a solution method.
  • An aqueous solution of transition metal acetate (Co (C 2 H 3 O 3 ) 2 .4H 2 O) and ammonium paratungstate were mixed.
  • transition metal acetate Co (C 2 H 3 O 3 ) 2 .4H 2 O
  • ammonium paratungstate were mixed.
  • the peak of the bcc W phase was observed, and a W alloy powder in which Co was uniformly and forcibly dissolved was obtained.
  • Sample No. 3 is a material of the present invention obtained by a solution method.
  • An aqueous solution of transition metal acetate (Co (C 2 H 3 O 3 ) 2 .4H 2 O) and ammonium paratungstate were mixed so that the composition was 80 mol% W-20 mol% Co.
  • transition metal acetate Co (C 2 H 3 O 3 ) 2 .4H 2 O
  • ammonium paratungstate were mixed so that the composition was 80 mol% W-20 mol% Co.
  • the bcc W phase was observed, and a W alloy powder in which Co was forcibly solid-solved was obtained.
  • the equilibrium phase at the hydrogen thermal reduction temperature of 1073 K of this composition is the W phase and the Co 7 W 6 phase.
  • Sample No. 4 and sample no. 5 is a material of the present invention obtained by a solution method. It was confirmed that a W alloy powder in which Co was uniformly and solid-solved up to the composition of 60 mol% W-40 mol% Co was obtained. When the solution method was applied, forced solid solution alloy powder could be produced in a non-equilibrium state without forming an equilibrium phase Co 7 W 6 phase up to this composition.
  • Sample No. 6 is a material of the present invention obtained by a solution method in which a part of a Co (C 2 H 3 O 3) 2 .4H 2 O aqueous solution is replaced with an Fe (OH) (C 2 H 3 OO) 2 aqueous solution. . It has been found that forced solid solution alloy powder can be produced even if a part of Co is replaced by Fe.
  • Sample No. 7 is a part of Co (C 2 H 3 O 3 ) 2 .4H 2 O aqueous solution, Fe (OH) (C 2 H 3 OO) 2 , Mn (CH 3 COO) 2 .4H 2 O and Ni (C It is the material of the present invention obtained by a solution method in which the solution is replaced with an aqueous solution of 2 H 3 O 3 ) 2 .xH 2 O. It has been found that forced solid solution alloy powder can be produced even if a part of Co is replaced by Fe, Mn, and Ni.
  • Sample No. 8 is a material of the present invention obtained by a solution method in which a part of a Co (C 2 H 3 O 3 ) 2 .4H 2 O aqueous solution is replaced with a Ni (C 2 H 3 O 3) 2 .xH 2 O aqueous solution. It is. Even if a part of Co was replaced by Ni, forced solid solution alloy powder could be produced.
  • Sample No. 9 is a part of an aqueous solution of Co (C 2 H 3 O 3 ) 2 .4H 2 O, Fe (OH) (C 2 H 3 OO) 2 and Ni (C 2 H 3 O 3 ) 2 .xH 2 O. It is this invention material obtained by the solution method replaced with the aqueous solution. The forced solid solution alloy powder could be produced even if a part of Co was replaced with a composite of Fe and Ni.
  • Sample No. 10 is a comparative material obtained by the solution method. With this composition of 10 mol% W-90 mol% Co, Co 3 W as an equilibrium phase finally precipitated as the second phase. Therefore, if the amount of Co is large, even if the solution method is used, the diffusion of W atoms in the Co lattice is easy, so that it is impossible to produce a forced solid solution.
  • Sample No. 11 is a comparative material obtained by the solution method. With this composition of 50 mol% W-50 mol% Co, Co 7 W 6 which is an equilibrium phase finally precipitated as the second phase. Therefore, even in this composition, since W atoms diffuse, it was impossible to produce a forced solid solution.
  • Sample No. 12 is a material of the present invention obtained by a solution method in which a part of a Co (C 2 H 3 O 3 ) 2 .4H 2 O aqueous solution is replaced with an Fe (OH) (C 2 H 3 OO) 2 aqueous solution. .
  • This is a forced solid solution alloy powder in which a part of Co is replaced with a small amount of Fe.
  • Sample No. 13 is the material of the present invention obtained by a solution method in which a part of the Co (C 2 H 3 O 3 ) 2 .4H 2 O aqueous solution is replaced with an Fe (OH) (C 2 H 3 OO) 2 aqueous solution. .
  • the forced solid solution alloy powder could be produced without adding the Ni (C 2 H 3 O 3 ) 2 .xH 2 O aqueous solution shown in No. 8.
  • Sample No. 14 is the material of the present invention obtained by a solution method in which the entire Co (C 2 H 3 O 3) 2 .4H 2 O aqueous solution is replaced with an Fe (OH) (C 2 H 3 OO) 2 aqueous solution. Even if all were replaced with Fe, it was possible to produce forced solid solution alloy powder.
  • Sample No. 15 replaces all Co (C 2 H 3 O 3 ) 2 .4H 2 O aqueous solution with Fe (OH) (C 2 H 3 OO) 2 aqueous solution and Mn (CH 3 COO) 2 .4H 2 O aqueous solution. It is this invention material obtained by the solution method. Even if all of Co was replaced with Fe and Mn, forced solid solution alloy powder could be produced.
  • Invention material No. 1 in Table 2. 22-No. No. 27 was prepared by adding and mixing graphite to a tungsten alloy powder in which a transition metal was forcibly dissolved by a solution method. That is, transition metal acetates (Co (C 2 H 3 O 3 ) 2 .4H 2 O, Fe (OH) (C 2 H 3 OO) 2 , Mn (CH 3 COO) 2 .4H 2 O and / or Ni An aqueous solution of (C 2 H 3 O 3 ) 2 ⁇ xH 2 O) and an aqueous solution of ammonium paratungstate (5 (NH 4) 2 O ⁇ 12WO 3 ⁇ 5H 2 O) were mixed and then evaporated to dryness (or sprayed) Dried), the resulting solid was thermally decomposed into oxides at 823 K in the atmosphere, and reduced to hydrogen by reducing it to 1073 K in hydrogen gas for 1 h. Produced. Next, graphite was mixed with this tungsten alloy powder, and held in Ar
  • Sample No. 21 is WC carbide obtained by mixing graphite with WO 3 which is a conventional technique of powder metallurgy and carbonizing it at 1473K for 1 hour.
  • the metal phase was not included in the WC skeleton.
  • Sample No. 22, Sample No. 23, sample no. 24, Sample No. 25, Sample No. 26, Sample No. 27 and no. 28 is the material of the present invention obtained by the solution method and carbonization. A unique tissue in which a metal phase was encapsulated in the WC skeleton was obtained. This metal phase is useful for resource saving of tungsten and for improving the mechanical properties of the carbide. Sample No. 22, Sample No. 23, sample no. 24 and sample no. It was found that many metal phases were included in the order of 25.
  • Sample No. 26, Sample No. 27 and no. 28 is a carbide whose cost is reduced by substituting cobalt of the metal phase contained therein with iron, iron-manganese and nickel.
  • Sample No. 29 and No. 30 is a comparative material obtained by the solution method and carbonization.
  • Sample No. When the amount of cobalt is larger than the amount of tungsten as in 29, tungsten is diffused in cobalt during the production of the tank stainless alloy powder, and Co 3 W and Co 7 W 6 in an equilibrium phase are generated. As a result, when this alloy powder is carbonized, the metal phase surrounds the carbide, and the metal phase cannot be included in the carbide.
  • 31 and no. No. 32 was prepared by adding and mixing graphite to a tungsten alloy powder in which a transition metal was forcibly dissolved by a solution method. That is, in the same manner as Sample No. 26, transition metal acetate (Co (C 2 H 3 O 3 ) 2 .4H 2 O aqueous solution, Fe (OH) (C 2 H 3 OO) 2 aqueous solution and ammonium paratungstate After mixing (5 (NH 4 ) 2 O ⁇ 12WO 3 ⁇ 5H 2 O) aqueous solution, it was evaporated to dryness (or spray drying), and the resulting solid was thermally decomposed into oxides at 823 K in the atmosphere.
  • transition metal acetate Co (C 2 H 3 O 3 ) 2 .4H 2 O aqueous solution, Fe (OH) (C 2 H 3 OO) 2 aqueous solution and ammonium paratungstate
  • a tank stainless alloy powder in which transition metal elements were forcibly dissolved was prepared by holding it at 1073 K in hydrogen gas for 1 h, and then graphite was mixed with this tungsten alloy powder, and 1473 K in Ar.
  • a tungsten carbide was produced by holding for 1 h at a specific structure in which a Co—Fe solid solution phase was encapsulated in the WC skeleton.
  • 33 and no. No. 34 was prepared by adding and mixing graphite to a tungsten alloy powder in which Fe and Mn were forcibly dissolved by a solution method. That is, Fe (OH) (C 2 H 3 OO) 2 aqueous solution, Mn (CH 3 COO) 2 .4H 2 O aqueous solution, ammonium paratungstate (5 (NH 4 ) 2 O.12WO 3 .5H 2 O) aqueous solution After mixing, after evaporating to dryness (or spray drying), the resulting solid was thermally decomposed into oxides at 823 K in the atmosphere, and then heated to 1073 K in hydrogen gas for 1 h for hydrothermal reduction Thus, a tank stainless alloy powder in which the transition metal element was forcibly dissolved was prepared.
  • FIG. The result of having observed 23 invention materials by EPMA is shown. From the SEM image and the corresponding X-ray images of W and C, it was found that a WC skeleton was formed. Further, it can be understood from the X-ray image of Co that a metal phase is formed in the WC skeleton. That is, (A) is an SEM image. The part that appears white is the WC skeleton, and the part that appears black is a domain made of metal Co. The Co domain inevitably grows when sintered at 1623 K for 3.6 ks, but it remains below 3 mm. (B) is an X-ray image of W. The formation of the WC skeleton is shown. (C) is an X-ray image of Co.
  • (D) is an X-ray image of C.
  • the formation of the WC skeleton is shown.
  • the formation of this metal phase is effective for reducing the amount of tungsten used and also improves the mechanical properties. Therefore, the cemented carbide in which this new WC carbide is dispersed is suitable as an abrasion resistant material.
  • the cemented carbide can be manufactured by a known manufacturing method, that is, by sintering the tungsten carbide of the present invention together with Co powder.
  • FIG. An EPMA photograph is shown in a cemented carbide made as a prototype by adding 3.6 mass of binder phase Co to 34 invention materials and sintering at 1623 K for 3.6 ks. It was found that a Fe—Mn solid solution phase was formed in the WC skeleton in the cemented carbide, and a part of the binder phase Co was distributed to the Fe—Mn solid solution phase during sintering. The Vickers hardness was Hv1945, indicating a very high hardness.
  • (A) is an SEM image.
  • the part that appears white is the WC skeleton, and the part that appears black is the domain composed of the Fe—Mn solid solution phase. The metal domain inevitably grows during sintering, but it remains below 1 mm.
  • the trace of the Vickers hardness test of this SEM image is shown.
  • the Vickers hardness was Hv1945, indicating a very high hardness. It was also found that cracks did not occur at the tip of the Vickers hardness test indentation and that the toughness was good.
  • (B) is an X-ray image of W. The formation of the WC skeleton is shown.
  • (C) shows the formation of a Fe—Mn solid solution domain which is an X-ray image of Fe.
  • D is an X-ray image of Co. It shows that a part of the binder phase Co is distributed to the Fe—Mn solid solution domains during sintering.
  • E is an X-ray image of C. The formation of the WC skeleton is shown.
  • F is an X-ray image of Mn. The formation of Fe-Mn solid solution domains is shown. The reason why the WC carbide including the metal domain exhibits such a high hardness is that in the present invention, the WC skeleton has succeeded in creating a microstructure that restrains deformation of the metal domain.
  • the alloy powder of the present invention has the transition metal element uniformly and uniformly dissolved in the tungsten lattice. Therefore, as an alloy powder in which a part of tungsten is replaced with a transition metal element, it can be widely used in applications for saving tungsten resources such as tungsten carbide raw material for cemented carbide.
  • the tungsten alloy powder of the present invention forms tungsten carbide in the same manner as the tungsten powder, and can produce a cemented carbide sintered with the binder phase Co.
  • Sample No. It is a figure which shows the result of having observed the metal phase inclusion tungsten carbide in 23 material of this invention by EMPA.
  • A is a SEM image
  • the white part is a WC skeleton
  • the black part is a domain made of Co.
  • B is an X-ray image of W and shows the formation of the WC skeleton.
  • C is an X-ray image of Co, showing the formation of a Co domain in the WC skeleton.
  • D is an X-ray image of C, showing the formation of a WC skeleton.
  • Sample No. It is a figure which shows the result of having observed the metal phase inclusion tungsten carbide in 34 this invention materials by EMPA.
  • (A) is an SEM image, the white portion is a WC skeleton, and the black portion is a domain composed of a Fe—Mn solid solution phase.
  • (B) is an X-ray image of W and shows the formation of a WC skeleton.
  • (C) is an X-ray image of Fe and shows the formation of a Fe—Mn solid solution domain.
  • (D) is an x-ray image of Co and shows that a part of the binder phase Co is distributed to the Fe—Mn solid solution domain during sintering.
  • (E) is an X-ray image of C and shows the formation of a WC skeleton.
  • (F) is an X-ray image of Mn, showing the formation of Fe—Mn solid solution domains.

Abstract

Disclosed is a powder of a tungsten alloy with a transition metal dissolved therein as a solid solution that is suitable as a material for a cemented carbide represented by formula [1] and a material for a catalyst.  The powder of the tungsten alloy is characterized in that at least one transition metal element selected from the group consisting of cobalt, iron, manganese, and nickel is dissolved as a solid solution in a tungsten grating and a peak derived from a bcc tungsten phase appears in an X-ray diffraction diagram. Formula [1]: M-W wherein M represents one or more elements selected from Co, Fe, Mn, or Ni. The use of the powder of the tungsten alloy can provide a tungsten carbide with a transition metal dissolved therein as a solid solution in which a solid solution phase of at least one transition metal element selected from the group consisting of cobalt, iron, manganese, and nickel, tungsten, and carbon is included in a tungsten carbide skeleton, and a tungsten carbide diffused cemented carbide.

Description

遷移金属固溶タングステン合金粉末及びその製造方法Transition metal solid solution tungsten alloy powder and method for producing the same
　本発明は遷移金属固溶タングステン合金粉末及びその製造方法に関する。 The present invention relates to a transition metal solid solution tungsten alloy powder and a method for producing the same.
　タングステンは高い融点と弾性率を有し、フィラメント材料やタングステン炭化物（ＷＣ）の原料として有用である。しかしながら、その資源は専ら中国に偏在していることから、中国の国内需要の急増に伴い、その価格が高騰する傾向にある。タングステンを省資源化した材料を開発するためには、タングステンの一部を遷移金属元素で代替する必要がある。 Tungsten has a high melting point and elastic modulus, and is useful as a raw material for filament materials and tungsten carbide (WC). However, since the resources are mainly unevenly distributed in China, the price tends to rise with the rapid increase in domestic demand in China. In order to develop a material that saves tungsten, it is necessary to replace a part of tungsten with a transition metal element.
　しかしながら、タングステンはその融点の高さから溶融製造は困難である。また、形状付与のために粉末冶金技術を用いる場合にも、タングステン粉末と遷移金属元素の素粉末混合法では、合金化が進行しない問題がある。さらに、合金粉末製造のためのアトマイズ法の適用も困難である。 However, it is difficult to melt and manufacture tungsten because of its high melting point. In addition, when using powder metallurgy technology for imparting a shape, there is a problem that alloying does not proceed in the powder mixing method of tungsten powder and transition metal element. Furthermore, it is difficult to apply the atomizing method for producing the alloy powder.
　他方、従来から金属塩又は金属水酸化物の共沈法を用いてタングステン合金粉末を製造する方法が知られている（特許文献１、特許文献２）。 On the other hand, a method for producing a tungsten alloy powder by using a coprecipitation method of a metal salt or a metal hydroxide is conventionally known (Patent Document 1, Patent Document 2).
特表２００２－５２７６２６号公報JP-T-2002-527626 米国特許第４９１３７３１号明細書U.S. Pat. No. 4,913,731
　しかしながら、特許文献１、２記載の製造方法では共沈という操作の関係上、合金粉末にはタングステン相及び遷移金属元素を合金化したタングステン相以外に、遷移金属元素の相が含まれ、合金化が十分進行していなかった。 However, due to the operation of coprecipitation in the production methods described in Patent Documents 1 and 2, the alloy powder contains a transition metal element phase in addition to the tungsten phase and the tungsten phase alloyed with the transition metal element. Was not progressing sufficiently.
　本発明はかかる問題点に鑑み、遷移金属元素を固溶（強制固溶を含む）した新規タングステン合金粉末及びその製造方法を提供することを課題とする。 In view of such problems, an object of the present invention is to provide a novel tungsten alloy powder in which a transition metal element is dissolved (including forced solid solution) and a method for producing the same.
　上記目標を達成するため、本発明者は、鋭意研究を重ねた結果、水溶液中にタングステンイオンと遷移金属イオンをイオンレベルで均一・一様化し、蒸発乾固又は噴霧乾燥した後、熱分解させ、水素熱還元を行ってタングステン粉末を得ると、遷移金属元素を完全に強制固溶したタングステン合金粉末を作製できることを見出し、ここに本発明をなしたものである。 In order to achieve the above goal, the present inventor has conducted extensive research, and as a result, the tungsten ion and the transition metal ion are uniformly and uniformly formed in an aqueous solution at the ionic level, and after evaporating to dryness or spray drying, thermal decomposition is performed. The inventors have found that when a tungsten powder is obtained by performing hydrogen thermal reduction, a tungsten alloy powder in which the transition metal element is completely forcibly dissolved can be produced, and the present invention is made here.
　すなわち、本発明はコバルト、鉄、マンガン及びニッケルの群から選ばれる少なくとも１種の遷移金属元素がタングステン格子中に固溶されてなり、Ｘ線回折図形にｂｃｃタングステン相ピークが認められる式［１］で示される遷移金属固溶タングステン合金粉末にある。
　　式［１］：Ｍ－Ｗ（但し、ＭはＣｏ，Ｆｅ，ＭｎまたはＮｉから選ばれる１種以上を示す）
　本発明の遷移金属固溶タングステン合金粉末には単一遷移金属がタングステンに固溶した、１）コバルトがタングステン格子中に固溶されてなり、Ｃｏ－Ｗで示される遷移金属固溶タングステン合金粉末、２）鉄がタングステン格子中に固溶されてなり、式：Ｆｅ－Ｗで示される遷移金属固溶タングステン合金粉末、３）ニッケルがタングステン格子中に固溶されてなり、式：Ｎｉ－Ｗで示される遷移金属固溶タングステン合金粉末が挙げられる。 That is, according to the present invention, at least one transition metal element selected from the group consisting of cobalt, iron, manganese and nickel is dissolved in a tungsten lattice, and the formula [1 In the transition metal solid solution tungsten alloy powder.
Formula [1]: MW (wherein M represents one or more selected from Co, Fe, Mn or Ni)
In the transition metal solid solution tungsten alloy powder of the present invention, a single transition metal is dissolved in tungsten. 1) Cobalt is dissolved in a tungsten lattice, and a transition metal solid solution tungsten alloy powder represented by Co—W is obtained. 2) Iron is dissolved in tungsten lattice, transition metal solid solution tungsten alloy powder represented by the formula: Fe-W, 3) Nickel is dissolved in tungsten lattice, formula: Ni-W The transition metal solid solution tungsten alloy powder shown by these is mentioned.
　上記コバルト、鉄、ニッケルの一部は、他の遷移金属である鉄、マンガン及びニッケルの群から選ばれる１種以上と置換することができ、複合遷移金属固溶タングステン粉末を得ることができる。その内、４）コバルトの一部を、鉄、マンガン、鉄－マンガン及びニッケルの群から選ばれる１種以上と置換した式［２］：Ｃｏ－Ｍ１－Ｗ（但し、Ｍ１はＦｅ，ＭｎまたはＮｉから選ばれる１種以上を示す）で示される遷移金属固溶タングステン合金粉末、５）鉄がタングステン格子中に固溶されてなり、鉄の一部がコバルト、マンガン及びニッケルの群から選ばれる１種以上と置換した式［３］：Ｆｅ－Ｍ２－Ｗ（但し、Ｍ２は，Ｃｏ，ＭｎまたはＮｉから選ばれる１種以上を示す）で示される遷移金属固溶タングステン合金粉末が好ましい。 A part of the cobalt, iron, and nickel can be substituted with one or more selected from the group of iron, manganese, and nickel, which are other transition metals, and a composite transition metal solid solution tungsten powder can be obtained. Among them, 4) Formula [2] in which a part of cobalt is substituted with one or more selected from the group consisting of iron, manganese, iron-manganese and nickel (where M1 is Fe, Mn or Transition metal solid solution tungsten alloy powder represented by 1) selected from Ni), 5) iron is dissolved in tungsten lattice, and a part of iron is selected from the group of cobalt, manganese and nickel A transition metal solid solution tungsten alloy powder represented by the formula [3]: Fe-M2-W (wherein M2 represents one or more selected from Co, Mn or Ni) substituted with one or more is preferable.
　タングステンに対する遷移金属の固溶量はタングステンの等量モルまで可能である。固溶元素としては、コバルトの場合、タングステン６０～９０ｍｏｌ％に対しコバルト４０～１０ｍｏｌ％が適当であり、他の遷移金属も同様である。 The amount of transition metal dissolved in tungsten can be up to the equivalent mole of tungsten. As a solid solution element, in the case of cobalt, 40 to 10 mol% of cobalt is appropriate with respect to 60 to 90 mol% of tungsten, and the same applies to other transition metals.
　本発明は、上記遷移金属固溶タングステン粉末を得る製造方法を提供することを第２の目的とするものであり、タングステンイオンを含む水溶液と、コバルト、鉄、鉄―マンガン及びニッケルの群から選ばれる少なくとも１種の遷移金属イオンを含む水溶液を、タングステンイオンが６０ｍｏｌ％以上、遷移金属イオンが４０ｍｏｌ％以下の比率で混合し、該混合水溶液を蒸発乾固させるか又は噴霧乾燥させ、得られた固形物を熱分解した後水素熱還元することによって、遷移金属元素を固溶した式［１］で示される遷移金属固溶タングステン合金粉末
　　式［１］：Ｍ－Ｗ（但し、ＭはＣｏ、Ｆｅ、ＭｎまたはＮｉから選ばれる１種以上を示す）
を製造するようにしたことを特徴とする遷移金属固溶タングステン合金粉末の製造方法を提供するものである。 The second object of the present invention is to provide a production method for obtaining the transition metal solid solution tungsten powder, which is selected from the group consisting of an aqueous solution containing tungsten ions and cobalt, iron, iron-manganese and nickel. An aqueous solution containing at least one kind of transition metal ions was mixed at a ratio of 60 mol% or more of tungsten ions and 40 mol% or less of transition metal ions, and the mixed aqueous solution was evaporated to dryness or spray dried. The transition metal solid solution tungsten alloy powder represented by the formula [1] in which the transition metal element is solid-solved by thermally decomposing the solid material and then hydrothermally reducing the formula [1]: MW (where M is Co, One or more selected from Fe, Mn or Ni)
The present invention provides a method for producing a transition metal solid solution tungsten alloy powder characterized in that the above is produced.
　本発明においては、タングステンイオンを含む水溶液がパラタングステン酸アンモニウム（５( ＮＨ4)2 Ｏ・１２ＷＯ3 ・５Ｈ2 Ｏ）水溶液であり、コバルト、鉄、マンガン及びニッケルの群から選ばれる少なくとも一種の遷移金属イオンを含む水溶液が遷移金属錯体塩水溶液であるのが好ましい。遷移金属錯体塩として酢酸塩（Ｆｅ(ＯＨ)(Ｃ2Ｈ3ＯＯ) 2 、Ｃｏ( Ｃ2Ｈ3Ｏ3)2・４Ｈ2Ｏ、Ｍｎ( ＣＨ3ＣＯＯ）2・４Ｈ2Ｏ、Ｎｉ(Ｃ2Ｈ3Ｏ3)2・ｘＨ2Ｏ）、および硫酸塩（ＦｅＳＯ4・７Ｈ2 Ｏ、ＣｏＳＯ4・７Ｈ2 Ｏ、ＮｉＳＯ4・６Ｈ2Ｏ、ＭｎＳＯ4・５Ｈ2 Ｏ）を用いることができる。 In the present invention, the aqueous solution containing tungsten ions is an aqueous solution of ammonium paratungstate (5 (NH 4) 2 O · 12WO 3 · 5H 2 O), which is at least one selected from the group consisting of cobalt, iron, manganese and nickel. The aqueous solution containing transition metal ions is preferably a transition metal complex salt aqueous solution. As transition metal complex salts, acetate (Fe (OH) (C 2 H 3 OO) 2 , Co (C 2 H 3 O 3 ) 2 .4H 2 O, Mn (CH 3 COO) 2 .4H 2 O, Ni ( C 2 H 3 O 3 ) 2 · xH 2 O) and sulfates (FeSO 4 · 7H 2 O, CoSO 4 · 7H 2 O, NiSO 4 · 6H 2 O, MnSO 4 · 5H 2 O) it can.
　本発明で得られるタングステン合金粉末は、遷移金属元素がタングステン格子中に固溶されてなり、Ｘ線回折図形にｂｃｃ相ピークが認められることを特徴とするので、この遷移金属固溶タングステン合金粉末ではタングステン粒界に実質的に遷移金属元素又はその金属化合物が存在しないことが分かる。 The tungsten alloy powder obtained by the present invention is characterized in that the transition metal element is dissolved in the tungsten lattice and the bcc phase peak is observed in the X-ray diffraction pattern. Then, it turns out that a transition metal element or its metal compound does not exist substantially in a tungsten grain boundary.
　本発明に係るタングステン合金粉末は、重量組成で示すと、式［１］で示される遷移金属固溶タングステン合金粉末
　　　式［１］：Ｍ－Ｗ（但し、ＭはＣｏ、Ｆｅ、ＭｎまたはＮｉから選ばれる１種以上を示す）
であって、コバルトを０．３～２０．８重量％含み、残部がタングステンからなるのを基本とするが、コバルトの全てあるいは一部を、鉄、マンガン及びニッケルの一種以上の元素で置換することにより形成される。ここで、コバルトを含めＭ成分がタングステン合金粉末の０．３重量％未満では省資源の効果が得られず、２０．８重量％を超えると、タンクステン粒界に第２相が析出し、遷移金属元素を固溶（強制固溶）したタングステン合金粉末にならないことが見られる。 When the tungsten alloy powder according to the present invention is expressed by weight composition, the transition metal solid solution tungsten alloy powder represented by the formula [1] Formula [1]: MW (where M is Co, Fe, Mn or Ni) One or more selected)
The cobalt is basically contained in an amount of 0.3 to 20.8% by weight and the balance is made of tungsten, but all or a part of cobalt is replaced with one or more elements of iron, manganese and nickel. Is formed. Here, if the M component including cobalt is less than 0.3% by weight of the tungsten alloy powder, the resource saving effect cannot be obtained, and if it exceeds 20.8% by weight, the second phase is precipitated at the tank stainless grain boundary, It can be seen that the tungsten alloy powder does not become a solid solution (forced solid solution) of the transition metal element.
　コバルトは、タングステンの格子位置に置換して存在することで、タングステンの代替元素として作用し、価格が高騰しているタングステンの省資源化に有効である。また、コバルトを固溶（強制固溶）することで触媒活性が高め、本発明合金粉末に触媒としての機能を付与することができる。
　他方、ニッケルは、コバルトと類似の機能をもち、コバルトよりも価格が安いことに特徴を有する。また、ニッケルはコバルト以上に触媒活性を付与する。鉄は、タンクステン粉末の強度を向上させ、しかも安価であることに特徴を有する。また、鉄及び鉄-マンガンはその変態的特徴を有効に利用することができ、超硬合金金型の破壊靱性の改善に役立てることができる。 Cobalt is present in substitution for the lattice position of tungsten, so that it acts as an alternative element for tungsten and is effective for resource saving of tungsten, which is rising in price. Moreover, catalytic activity can be increased by dissolving cobalt in a solid solution (forced solid solution), and the alloy powder of the present invention can be given a function as a catalyst.
On the other hand, nickel has a function similar to that of cobalt and is characterized by a lower price than cobalt. Nickel also imparts catalytic activity over cobalt. Iron is characterized by improving the strength of tank stainless powder and being inexpensive. In addition, iron and iron-manganese can effectively utilize their transformation characteristics, and can be used to improve the fracture toughness of the cemented carbide mold.
　遷移金属イオンを含む水溶液としては、金属錯体塩、例えば、鉄、ニッケル、マンガンおよびコバルトの酢酸塩（Ｃｏ( Ｃ2Ｈ3Ｏ3)2・４Ｈ2Ｏ、Ｆｅ(ＯＨ)(Ｃ2Ｈ3ＯＯ) 2 、Ｍｎ( ＣＨ3ＣＯＯ）2・４Ｈ2Ｏ、Ｎｉ(Ｃ2Ｈ3Ｏ3)2・ｘＨ2Ｏ）を用いると、水溶性であり、かつ、有害物質を発生させず、環境負荷が小さい。また、鉄、ニッケルおよびコバルトの遷移金属硫酸塩（ＣｏＳＯ4・７Ｈ2 Ｏ、ＦｅＳＯ4・７Ｈ2 Ｏ、ＮｉＳＯ4・６Ｈ2 Ｏ）の使用も循環型社会実現のために有効である。一般的に、銅の電解精製プロセスでは、電解液中の硫酸中に、鉄、ニッケルおよびコバルトの遷移金属が濃縮される。したがって、銅の電解精製で発生した廃液を、本発明のタングステン合金粉末の原料として使用することができ、かつ、蒸発乾固あるいは噴霧乾燥時に発生した硫酸も、副製品として有効利用することができる。 Examples of the aqueous solution containing transition metal ions include metal complex salts such as iron, nickel, manganese and cobalt acetates (Co (C 2 H 3 O 3 ) 2 .4H 2 O, Fe (OH) (C 2 H 3 OO) 2 , Mn (CH 3 COO) 2 .4H 2 O, Ni (C 2 H 3 O 3 ) 2 .xH 2 O) are water-soluble and do not generate harmful substances. The load is small. Use of transition metal sulfates of iron, nickel and cobalt (CoSO 4 · 7H 2 O, FeSO 4 · 7H 2 O , NiSO 4 · 6H 2 O) is also effective for realizing a recycling society. In general, copper electrorefining processes concentrate iron, nickel and cobalt transition metals in sulfuric acid in the electrolyte. Therefore, the waste liquid generated by electrolytic refining of copper can be used as a raw material for the tungsten alloy powder of the present invention, and sulfuric acid generated during evaporation to dryness or spray drying can also be effectively used as a by-product. .
　以下、本発明を代表的実施例に基づいて説明するが、遷移金属イオンを含む水溶液としては、各種金属錯体塩を単独で、または２種以上を併用して用いることによりタングステン金属に１種または２種以上の遷移金属を固溶させ、タングステン金属の一部と置換させることができるのは実施例より当業者には明らかである。 Hereinafter, the present invention will be described based on representative examples. As an aqueous solution containing transition metal ions, various metal complex salts may be used alone or in combination of two or more to form tungsten metal or It will be apparent to those skilled in the art from the examples that two or more transition metals can be dissolved and replaced with part of the tungsten metal.
　表１に示す化学成分（mol％）を有する、従来材（Ｎｏ．１）、本発明材（Ｎｏ．２～Ｎｏ．９）、比較材（Ｎｏ．１０、Ｎｏ．１１）を作製し、Ｘ線回折とＥＰＭＡにより、強制固溶体生成の可否、第２相析出の有無を調べた。 Conventional materials (No. 1), inventive materials (No. 2 to No. 9), and comparative materials (No. 10, No. 11) having chemical components (mol%) shown in Table 1 were prepared, and X By means of line diffraction and EPMA, the possibility of forced solid solution formation and the presence or absence of second phase precipitation were examined.
Figure JPOXMLDOC01-appb-T000001
Figure JPOXMLDOC01-appb-T000001
　表１において、溶液法とは本発明プロセスのことであり、遷移金属酢酸塩（Ｃｏ( Ｃ2Ｈ3Ｏ3)2・４Ｈ2Ｏ、Ｆｅ(ＯＨ)(Ｃ2Ｈ3ＯＯ) 2 、Ｍｎ( ＣＨ3ＣＯＯ）2・４Ｈ2Ｏ及び／又はＮｉ(Ｃ2Ｈ3Ｏ3)2・ｘＨ2Ｏ）の水溶液とパラタングステン酸アンモニウム（５( ＮＨ4)2 Ｏ・１２ＷＯ3 ・５Ｈ2 Ｏ）の水溶液を混合した後、蒸発乾固（噴霧乾燥でもよい）させ、得られた固形物を大気中８２３Ｋで酸化物に熱分解した後、水素ガス中１０７３Ｋで１ｈ保持することにより水素熱還元してタンクステン合金粉末を得る方法である。 In Table 1, the solution method is the process of the present invention, and includes transition metal acetates (Co (C 2 H 3 O 3 ) 2 .4H 2 O, Fe (OH) (C 2 H 3 OO) 2 , Mn An aqueous solution of (CH 3 COO) 2 · 4H 2 O and / or Ni (C 2 H 3 O 3 ) 2 · xH 2 O) and ammonium paratungstate (5 (NH 4) 2 O · 12WO 3 · 5H 2 O ) And then evaporated to dryness (may be spray-dried), and the resulting solid was thermally decomposed to oxides at 823 K in the atmosphere, and then kept at 1073 K in hydrogen gas for 1 h for hydrothermal reduction. Thus, a tank stainless alloy powder is obtained.
　試料Ｎｏ．１は、粉末冶金の従来技術である素粉末混合法を適用して、表１の化学組成となるよう純コバルト粉末７．４２重量％と残部純タングステン粉末を秤量して混合後、２ｔｏｎ／ｃｍ2の圧力で圧縮成型した後、水素ガス中、１０７３Ｋで１ｈ保持して得た従来材である。第２相として純コバルト相が残留し、タングステンとの合金化は進行しなかった。 Sample No. 1 is a powder metallurgy, which is a conventional technique of powder metallurgy, and 7.42% by weight of pure cobalt powder and the remaining pure tungsten powder are weighed and mixed to obtain the chemical composition shown in Table 1, and then 2 ton / cm. This is a conventional material obtained by compression molding at a pressure of 2 and holding in hydrogen gas at 1073 K for 1 h. A pure cobalt phase remained as the second phase, and alloying with tungsten did not proceed.
　試料Ｎｏ．２は、溶液法によって得られた本発明材である。遷移金属酢酸塩（Ｃｏ( Ｃ2Ｈ3Ｏ3)2・４Ｈ2Ｏ）の水溶液とパラタングステン酸アンモニウムを混合した。得られた合金粉末のＸ線回折図形はｂｃｃＷ相のピークのみが見られ、Ｃｏを均一に強制固溶したＷ合金粉末が得られた。 Sample No. 2 is the material of the present invention obtained by a solution method. An aqueous solution of transition metal acetate (Co (C 2 H 3 O 3 ) 2 .4H 2 O) and ammonium paratungstate were mixed. In the X-ray diffraction pattern of the obtained alloy powder, only the peak of the bcc W phase was observed, and a W alloy powder in which Co was uniformly and forcibly dissolved was obtained.
　試料Ｎｏ．３は、溶液法によって得られた本発明材である。この８０ｍｏｌ％Ｗ－２０ｍｏｌ％Ｃｏの組成となるように遷移金属酢酸塩（Ｃｏ( Ｃ2Ｈ3Ｏ3)2・４Ｈ2Ｏ）の水溶液とパラタングステン酸アンモニウムを混合した。得られた合金粉末のＸ線回折図形はｂｃｃＷ相のピークのみがみられ、Ｃｏを均一に強制固溶したＷ合金粉末が得られた。この組成の水素熱還元温度、１０７３Ｋにおける平衡相は、Ｗ相とＣｏ7Ｗ6相である。溶液法によって、最初、水溶液中コバルトイオンとタングステンイオンとをイオンレベルで均一にすると、水素熱還元後もコバルトはタングステン格子中に捕獲され、平衡相Ｃｏ7Ｗ6相を形成できないことが確認された。すなわち、溶液法を適用すると、非平衡状態で強制固溶体合金粉末を製造できることが見出された。 Sample No. 3 is a material of the present invention obtained by a solution method. An aqueous solution of transition metal acetate (Co (C 2 H 3 O 3 ) 2 .4H 2 O) and ammonium paratungstate were mixed so that the composition was 80 mol% W-20 mol% Co. In the X-ray diffraction pattern of the obtained alloy powder, only the peak of the bcc W phase was observed, and a W alloy powder in which Co was forcibly solid-solved was obtained. The equilibrium phase at the hydrogen thermal reduction temperature of 1073 K of this composition is the W phase and the Co 7 W 6 phase. When cobalt ions and tungsten ions in an aqueous solution are first made uniform at the ion level by the solution method, it is confirmed that cobalt is trapped in the tungsten lattice even after hydrothermal reduction and an equilibrium phase Co 7 W 6 phase cannot be formed. It was. That is, it has been found that when a solution method is applied, a forced solid solution alloy powder can be produced in a non-equilibrium state.
　試料Ｎｏ．４及び試料Ｎｏ．５は、溶液法によって得られた本発明材である。この６０ｍｏｌ％Ｗ－４０ｍｏｌ％Ｃｏの組成まで、Ｃｏを均一に強制固溶したＷ合金粉末が得られることが確認された。溶液法を適用すると、この組成まで平衡相Ｃｏ7Ｗ6相を形成することなく、非平衡状態で強制固溶体合金粉末を製造できた。 Sample No. 4 and sample no. 5 is a material of the present invention obtained by a solution method. It was confirmed that a W alloy powder in which Co was uniformly and solid-solved up to the composition of 60 mol% W-40 mol% Co was obtained. When the solution method was applied, forced solid solution alloy powder could be produced in a non-equilibrium state without forming an equilibrium phase Co 7 W 6 phase up to this composition.
　試料Ｎｏ．６は、Ｃｏ( Ｃ2Ｈ3Ｏ3)2・４Ｈ2Ｏ水溶液の一部を、Ｆｅ(ＯＨ)(Ｃ2Ｈ3ＯＯ) 2 水溶液に置き換えた溶液法によって得られた本発明材である。Ｃｏの一部をＦｅで置換しても強制固溶体合金粉末の製造は可能であることが見出された。 Sample No. 6 is a material of the present invention obtained by a solution method in which a part of a Co (C 2 H 3 O 3) 2 .4H 2 O aqueous solution is replaced with an Fe (OH) (C 2 H 3 OO) 2 aqueous solution. . It has been found that forced solid solution alloy powder can be produced even if a part of Co is replaced by Fe.
　試料Ｎｏ．７はＣｏ( Ｃ2Ｈ3Ｏ3)2・４Ｈ2Ｏ水溶液の一部を、Ｆｅ(ＯＨ)(Ｃ2Ｈ3ＯＯ)2、Ｍｎ（ＣＨ3ＣＯＯ）2・４Ｈ2Ｏ及びＮｉ(Ｃ2Ｈ3Ｏ3)2・ｘＨ2Ｏの水溶液に置き換えた溶液法によって得られた本発明材である。Ｃｏの一部をＦｅ、Ｍｎ、Ｎｉで置換しても強制固溶体合金粉末の製造は可能であることが分かった。 Sample No. 7 is a part of Co (C 2 H 3 O 3 ) 2 .4H 2 O aqueous solution, Fe (OH) (C 2 H 3 OO) 2 , Mn (CH 3 COO) 2 .4H 2 O and Ni (C It is the material of the present invention obtained by a solution method in which the solution is replaced with an aqueous solution of 2 H 3 O 3 ) 2 .xH 2 O. It has been found that forced solid solution alloy powder can be produced even if a part of Co is replaced by Fe, Mn, and Ni.
　試料Ｎｏ．８は、Ｃｏ( Ｃ2Ｈ3Ｏ3)2・４Ｈ2Ｏ水溶液の一部を、Ｎｉ(Ｃ2Ｈ3Ｏ3)2・ｘＨ2Ｏ水溶液に置き換えた溶液法によって得られた本発明材である。Ｃｏの一部をＮｉで置換しても強制固溶体合金粉末の製造は可能であった。 Sample No. 8 is a material of the present invention obtained by a solution method in which a part of a Co (C 2 H 3 O 3 ) 2 .4H 2 O aqueous solution is replaced with a Ni (C 2 H 3 O 3) 2 .xH 2 O aqueous solution. It is. Even if a part of Co was replaced by Ni, forced solid solution alloy powder could be produced.
　試料Ｎｏ．９は、Ｃｏ( Ｃ2Ｈ3Ｏ3)2・４Ｈ2Ｏ水溶液の一部を、Ｆｅ(ＯＨ)(Ｃ2Ｈ3ＯＯ) 2 及びＮｉ(Ｃ2Ｈ3Ｏ3)2・ｘＨ2Ｏの水溶液に置き換えた溶液法によって得られた本発明材である。Ｃｏの一部をＦｅ及びＮｉを複合して置換しても強制固溶体合金粉末の製造は可能であった。 Sample No. 9 is a part of an aqueous solution of Co (C 2 H 3 O 3 ) 2 .4H 2 O, Fe (OH) (C 2 H 3 OO) 2 and Ni (C 2 H 3 O 3 ) 2 .xH 2 O. It is this invention material obtained by the solution method replaced with the aqueous solution. The forced solid solution alloy powder could be produced even if a part of Co was replaced with a composite of Fe and Ni.
　試料Ｎｏ．１０は、溶液法によって得られた比較材である。この１０ｍｏｌ％Ｗ－９０ｍｏｌ％Ｃｏの組成では、最終的に平衡相であるＣｏ3Ｗが第２相として析出した。したがって、Ｃｏ量が多いと、溶液法を用いても、Ｃｏ格子中でのＷ原子の拡散が容易であるため、強制固溶体の作製は不可能であった。 Sample No. 10 is a comparative material obtained by the solution method. With this composition of 10 mol% W-90 mol% Co, Co 3 W as an equilibrium phase finally precipitated as the second phase. Therefore, if the amount of Co is large, even if the solution method is used, the diffusion of W atoms in the Co lattice is easy, so that it is impossible to produce a forced solid solution.
　試料Ｎｏ．１１は、溶液法によって得られた比較材である。この５０ｍｏｌ％Ｗ－５０ｍｏｌ％Ｃｏの組成では、最終的に平衡相であるＣｏ7Ｗ6が第２相として析出した。したがって、この組成においても、Ｗ原子は拡散するため、強制固溶体の作製は不可能であった。 Sample No. 11 is a comparative material obtained by the solution method. With this composition of 50 mol% W-50 mol% Co, Co 7 W 6 which is an equilibrium phase finally precipitated as the second phase. Therefore, even in this composition, since W atoms diffuse, it was impossible to produce a forced solid solution.
　試料Ｎｏ．１２は、Ｃｏ( Ｃ2Ｈ3Ｏ3)2・４Ｈ2Ｏ水溶液の一部を、Ｆｅ(ＯＨ)(Ｃ2Ｈ3ＯＯ) 2水溶液に置き換えた溶液法によって得られた本発明材である。Ｃｏの一部を微量のFeで置換した強制固溶体合金粉末である。 Sample No. 12 is a material of the present invention obtained by a solution method in which a part of a Co (C 2 H 3 O 3 ) 2 .4H 2 O aqueous solution is replaced with an Fe (OH) (C 2 H 3 OO) 2 aqueous solution. . This is a forced solid solution alloy powder in which a part of Co is replaced with a small amount of Fe.
　試料Ｎｏ．１３は、Ｃｏ( Ｃ2Ｈ3Ｏ3)2・４Ｈ2Ｏ水溶液の一部を、Ｆｅ(ＯＨ)(Ｃ2Ｈ3ＯＯ) 2水溶液に置き換えた溶液法によって得られた本発明材である。No.8に示したＮｉ(Ｃ2Ｈ3Ｏ3)2・ｘＨ2Ｏ水溶液を加えずとも、強制固溶体合金粉末の製造は可能であった。 Sample No. 13 is the material of the present invention obtained by a solution method in which a part of the Co (C 2 H 3 O 3 ) 2 .4H 2 O aqueous solution is replaced with an Fe (OH) (C 2 H 3 OO) 2 aqueous solution. . The forced solid solution alloy powder could be produced without adding the Ni (C 2 H 3 O 3 ) 2 .xH 2 O aqueous solution shown in No. 8.
　試料Ｎｏ．１４は、Ｃｏ( Ｃ2Ｈ3Ｏ3)2・４Ｈ2Ｏ水溶液の全てを、Ｆｅ(ＯＨ)(Ｃ2Ｈ3ＯＯ) 2水溶液に置き換えた溶液法によって得られた本発明材である。全てをFeで置換しても強制固溶体合金粉末の製造は可能であった。 Sample No. 14 is the material of the present invention obtained by a solution method in which the entire Co (C 2 H 3 O 3) 2 .4H 2 O aqueous solution is replaced with an Fe (OH) (C 2 H 3 OO) 2 aqueous solution. Even if all were replaced with Fe, it was possible to produce forced solid solution alloy powder.
　試料Ｎｏ．１５は、Ｃｏ( Ｃ2Ｈ3Ｏ3)2・４Ｈ2Ｏ水溶液の全てを、Ｆｅ(ＯＨ)(Ｃ2Ｈ3ＯＯ) 2水溶液及びＭｎ（ＣＨ3ＣＯＯ）2・４Ｈ2Ｏ水溶液に置き換えた溶液法によって得られた本発明材である。Ｃｏの全てをＦｅ及びＭｎで置換しても強制固溶体合金粉末の製造は可能であった。 Sample No. 15 replaces all Co (C 2 H 3 O 3 ) 2 .4H 2 O aqueous solution with Fe (OH) (C 2 H 3 OO) 2 aqueous solution and Mn (CH 3 COO) 2 .4H 2 O aqueous solution. It is this invention material obtained by the solution method. Even if all of Co was replaced with Fe and Mn, forced solid solution alloy powder could be produced.
　　［タンクステン炭化物製造例］
　表２に示す化学成分（ｗｔ％）を有する、従来材（Ｎｏ．２１）、本発明材（Ｎｏ．２２～Ｎｏ．２８、Ｎｏ．３１～Ｎｏ．３４）、比較材（Ｎｏ．２９、Ｎｏ．３０）を作製した。 [Production example of tank stainless carbide]
Conventional materials (No. 21), inventive materials (No. 22 to No. 28, No. 31 to No. 34), and comparative materials (No. 29, No.) having chemical components (wt%) shown in Table 2. 30) was produced.
Figure JPOXMLDOC01-appb-T000002
Figure JPOXMLDOC01-appb-T000002
　表２中の本発明材Ｎｏ．２２～Ｎｏ．２７は、溶液法による遷移金属を強制固溶したタングステン合金粉末に、グラファイトを添加混合して作製した。すなわち、遷移金属酢酸塩（Ｃｏ( Ｃ2Ｈ3Ｏ3)2・４Ｈ2Ｏ、Ｆｅ(ＯＨ)(Ｃ2Ｈ3ＯＯ) 2 、Ｍｎ( ＣＨ3ＣＯＯ）2・４Ｈ2Ｏ及び／又はＮｉ(Ｃ2Ｈ3Ｏ3)2・ｘＨ2Ｏ）の水溶液とパラタングステン酸アンモニウム（５( ＮＨ4)2 Ｏ・１２ＷＯ3 ・５Ｈ2 Ｏ）の水溶液を混合した後、蒸発乾固（又は噴霧乾燥）させ、得られた固形物を大気中８２３Ｋで酸化物に熱分解し、水素ガス中１０７３Ｋで１ｈ保持することにより水素熱還元して、遷移金属元素を強制固溶したタンクステン合金粉末を作製した。
　次に、このタングステン合金粉末に、グラファイトを混合し、Ａｒ中、１４７３Ｋで１ｈ保持してタングステン炭化物を作製した。 Invention material No. 1 in Table 2. 22-No. No. 27 was prepared by adding and mixing graphite to a tungsten alloy powder in which a transition metal was forcibly dissolved by a solution method. That is, transition metal acetates (Co (C 2 H 3 O 3 ) 2 .4H 2 O, Fe (OH) (C 2 H 3 OO) 2 , Mn (CH 3 COO) 2 .4H 2 O and / or Ni An aqueous solution of (C 2 H 3 O 3 ) 2 · xH 2 O) and an aqueous solution of ammonium paratungstate (5 (NH 4) 2 O · 12WO 3 · 5H 2 O) were mixed and then evaporated to dryness (or sprayed) Dried), the resulting solid was thermally decomposed into oxides at 823 K in the atmosphere, and reduced to hydrogen by reducing it to 1073 K in hydrogen gas for 1 h. Produced.
Next, graphite was mixed with this tungsten alloy powder, and held in Ar at 1473 K for 1 h to produce tungsten carbide.
　試料Ｎｏ．２１は、粉末冶金の従来技術であるＷＯ3にグラファイトを混合し、１４７３Ｋで１ｈ、炭化したＷＣ炭化物である。ＷＣ骨格内に金属相は内包されていなかった。 Sample No. 21 is WC carbide obtained by mixing graphite with WO 3 which is a conventional technique of powder metallurgy and carbonizing it at 1473K for 1 hour. The metal phase was not included in the WC skeleton.
　試料Ｎｏ．２２、試料Ｎｏ．２３、試料Ｎｏ．２４、試料Ｎｏ．２５、試料Ｎo．２６、試料Ｎｏ．２７及びＮｏ．２８は溶液法と炭化によって得られた本発明材である。ＷＣ骨格中に金属相が内包された特異な組織が得られた。この金属相は、タングステンの省資源化に役立ち、かつ、炭化物の機械的性質の改善に役立つ。試料Ｎｏ．２２、試料Ｎｏ．２３、試料Ｎｏ．２４及び試料Ｎｏ．２５の順で金属相を多く内包することが分かった。 Sample No. 22, Sample No. 23, sample no. 24, Sample No. 25, Sample No. 26, Sample No. 27 and no. 28 is the material of the present invention obtained by the solution method and carbonization. A unique tissue in which a metal phase was encapsulated in the WC skeleton was obtained. This metal phase is useful for resource saving of tungsten and for improving the mechanical properties of the carbide. Sample No. 22, Sample No. 23, sample no. 24 and sample no. It was found that many metal phases were included in the order of 25.
　試料Ｎｏ．２６、試料Ｎｏ．２７及びＮｏ．２８は、内包する金属相のコバルトを鉄、鉄－マンガンおよびニッケルで置換し、価格を低減した炭化物である。 Sample No. 26, Sample No. 27 and no. 28 is a carbide whose cost is reduced by substituting cobalt of the metal phase contained therein with iron, iron-manganese and nickel.
　試料Ｎｏ．２９及びＮｏ．３０は、溶液法と炭化によって得られた比較材である。試料Ｎｏ．２９のようにタングステン量に比してコバルト量が多いと、タンクステン合金粉末の作製時に、コバルト中、タングステンが拡散して、平衡相のＣｏ3ＷやＣｏ7Ｗ6が生成する。その結果、この合金粉末を炭化すると炭化物の周囲を金属相が取り囲み、炭化物中に金属相を内包することができない。 Sample No. 29 and No. 30 is a comparative material obtained by the solution method and carbonization. Sample No. When the amount of cobalt is larger than the amount of tungsten as in 29, tungsten is diffused in cobalt during the production of the tank stainless alloy powder, and Co 3 W and Co 7 W 6 in an equilibrium phase are generated. As a result, when this alloy powder is carbonized, the metal phase surrounds the carbide, and the metal phase cannot be included in the carbide.
　表２中の本発明材Ｎｏ．３１及びＮｏ．３２は、溶液法による遷移金属を強制固溶したタングステン合金粉末に、グラファイトを添加混合して作製した。すなわち、試料No.26と同様にして、遷移金属酢酸塩（Ｃｏ( Ｃ2Ｈ3Ｏ3)2・４Ｈ2Ｏ水溶液、Ｆｅ(ＯＨ)(Ｃ2Ｈ3ＯＯ) 2 水溶液及びパラタングステン酸アンモニウム（５( ＮＨ4)2 Ｏ・１２ＷＯ3 ・５Ｈ2 Ｏ）水溶液を混合した後、蒸発乾固（又は噴霧乾燥）させ、得られた固形物を大気中８２３Ｋで酸化物に熱分解した後、水素ガス中１０７３Ｋで１ｈ保持することにより水素熱還元して、遷移金属元素を強制固溶したタンクステン合金粉末を作製した。次に、このタングステン合金粉末に、グラファイトを混合し、Ａｒ中、１４７３Ｋで１ｈ保持してタングステン炭化物を作製した。ＷＣ骨格中にCo-Fe固溶体相が内包された特異な組織が得られた。 Invention material No. 1 in Table 2. 31 and no. No. 32 was prepared by adding and mixing graphite to a tungsten alloy powder in which a transition metal was forcibly dissolved by a solution method. That is, in the same manner as Sample No. 26, transition metal acetate (Co (C 2 H 3 O 3 ) 2 .4H 2 O aqueous solution, Fe (OH) (C 2 H 3 OO) 2 aqueous solution and ammonium paratungstate After mixing (5 (NH 4 ) 2 O · 12WO 3 · 5H 2 O) aqueous solution, it was evaporated to dryness (or spray drying), and the resulting solid was thermally decomposed into oxides at 823 K in the atmosphere. A tank stainless alloy powder in which transition metal elements were forcibly dissolved was prepared by holding it at 1073 K in hydrogen gas for 1 h, and then graphite was mixed with this tungsten alloy powder, and 1473 K in Ar. A tungsten carbide was produced by holding for 1 h at a specific structure in which a Co—Fe solid solution phase was encapsulated in the WC skeleton.
　表２中の本発明材Ｎｏ．３３及びＮｏ．３４は、溶液法によるFe及びMnを強制固溶したタングステン合金粉末に、グラファイトを添加混合して作製した。すなわち、Ｆｅ(ＯＨ)(Ｃ2Ｈ3ＯＯ) 2 水溶液及びＭｎ（ＣＨ3ＣＯＯ）2・４Ｈ2Ｏ水溶液、パラタングステン酸アンモニウム（５( ＮＨ4)2 Ｏ・１２ＷＯ3 ・５Ｈ2 Ｏ）水溶液を混合した後、混合した後、蒸発乾固（又は噴霧乾燥）させ、得られた固形物を大気中８２３Ｋで酸化物に熱分解した後、水素ガス中１０７３Ｋで１ｈ保持することにより水素熱還元して、遷移金属元素を強制固溶したタンクステン合金粉末を作製した。次に、このタングステン合金粉末に、グラファイトを混合し、Ａｒ中、１４７３Ｋで１ｈ保持してタングステン炭化物を作製した。Ｃｏの全てをＦｅ、あるいはＦｅ及びＭｎで置換すると、金属Ｆｅ、あるいはＦｅ－Ｍｎ固溶体を内包するWC炭ＷＣ物の作製が可能であった。 Invention material No. 1 in Table 2. 33 and no. No. 34 was prepared by adding and mixing graphite to a tungsten alloy powder in which Fe and Mn were forcibly dissolved by a solution method. That is, Fe (OH) (C 2 H 3 OO) 2 aqueous solution, Mn (CH 3 COO) 2 .4H 2 O aqueous solution, ammonium paratungstate (5 (NH 4 ) 2 O.12WO 3 .5H 2 O) aqueous solution After mixing, after evaporating to dryness (or spray drying), the resulting solid was thermally decomposed into oxides at 823 K in the atmosphere, and then heated to 1073 K in hydrogen gas for 1 h for hydrothermal reduction Thus, a tank stainless alloy powder in which the transition metal element was forcibly dissolved was prepared. Next, graphite was mixed with this tungsten alloy powder, and held in Ar at 1473 K for 1 h to produce tungsten carbide. When all of Co was replaced with Fe, or Fe and Mn, it was possible to produce a WC charcoal WC product containing a metal Fe or Fe—Mn solid solution.
　図１に、試料Ｎｏ．２３の本発明材をＥＰＭＡ観察した結果を示す。ＳＥＭ像と対応するＷとＣのＸ線像より、ＷＣの骨格が形成されていることが分かった。また、ＣｏのＸ線像より、ＷＣの骨格中に金属相が形成されていることが理解できる。即ち、
　（ａ）は、SEM像である。白く見える部分がWC骨格であり、黒く見える部分が金属Ｃｏからなるドメインである。1623 Kで3.6 ks焼結時にCoドメインは不可避的に成長するが、なお、3mm以下を保っている。
　（ｂ）はＷのＸ線像である。ＷＣ骨格の形成を示す。
　（ｃ）はＣｏのＸ線像である。ＷＣ骨格中のＣｏドメインの形成を示す。
　（ｄ）はＣのＸ線像である。ＷＣ骨格の形成を示す。
　この金属相の形成がタングステンの使用量削減に有効であり、かつ、機械的特性も向上させる。したがって、この新規ＷＣ炭化物を分散した超硬合金は、耐摩耗材料として好適である。 In FIG. The result of having observed 23 invention materials by EPMA is shown. From the SEM image and the corresponding X-ray images of W and C, it was found that a WC skeleton was formed. Further, it can be understood from the X-ray image of Co that a metal phase is formed in the WC skeleton. That is,
(A) is an SEM image. The part that appears white is the WC skeleton, and the part that appears black is a domain made of metal Co. The Co domain inevitably grows when sintered at 1623 K for 3.6 ks, but it remains below 3 mm.
(B) is an X-ray image of W. The formation of the WC skeleton is shown.
(C) is an X-ray image of Co. The formation of Co domains in the WC skeleton is shown.
(D) is an X-ray image of C. The formation of the WC skeleton is shown.
The formation of this metal phase is effective for reducing the amount of tungsten used and also improves the mechanical properties. Therefore, the cemented carbide in which this new WC carbide is dispersed is suitable as an abrasion resistant material.
　超硬合金は公知の製造方法、すなわち本発明のタングステン炭化物をＣｏ粉末とともに焼結することによって製造できる。図２に、試料Ｎｏ．３４の本発明材に5mass%の結合相Ｃｏを加えて、1623 Kで3.6 ks焼結によって、試作した超硬合金中のEPMA写真を示した。超硬合金中、ＷＣ骨格にＦｅ－Ｍｎ固溶体相が形成され、結合相Ｃｏの一部は焼結中にこのＦｅ－Ｍｎ固溶体相に分配されることが分かった。ビッカ－ス硬さはHv1945であり、極めて高い硬さを示した。また、ビッカ－ス硬さ試験圧痕の先端にクラックは発生せず、靱性も良好であることが分かった。即ち、
　（ａ）は、SEM像である。白く見える部分がWC骨格であり、黒く見える部分がＦｅ－Ｍｎ固溶体相からなるドメインである。焼結時に金属ドメインは不可避的に成長するが、なお、1mm以下を保っている。このSEM像のビッカ－ス硬さ試験のあっ痕を示す。ビッカ－ス硬さはHv1945であり、極めて高い硬さを示した。また、ビッカ－ス硬さ試験圧痕の先端にクラックは発生せず、靱性も良好であることが分かった。
　（ｂ）は、ＷのＸ線像である。ＷＣ骨格の形成を示す。また、Ｗの一部はＦｅ－Ｍｎ固溶体ドメイン分配される。
　（ｃ）は、ＦｅのＸ線像であるＦｅ－Ｍｎ固溶体ドメインの形成を示す。
　（ｄ）は、ＣｏのＸ線像である。結合相Ｃｏの一部は焼結中にＦｅ－Ｍｎ固溶体ドメインに分配されることを示す。
　（ｅ）は、ＣのＸ線像である。ＷＣ骨格の形成を示す。
　（ｆ）は、ＭｎのＸ線像である。Ｆｅ－Ｍｎ固溶体ドメインの形成を示す。
　金属ドメインを内包するWC炭化物がこのような高い硬さを示す理由は，本発明において、WC骨格が金属ドメインの変形を拘束するマイクロ構造を創出することに成功したためである。 The cemented carbide can be manufactured by a known manufacturing method, that is, by sintering the tungsten carbide of the present invention together with Co powder. In FIG. An EPMA photograph is shown in a cemented carbide made as a prototype by adding 3.6 mass of binder phase Co to 34 invention materials and sintering at 1623 K for 3.6 ks. It was found that a Fe—Mn solid solution phase was formed in the WC skeleton in the cemented carbide, and a part of the binder phase Co was distributed to the Fe—Mn solid solution phase during sintering. The Vickers hardness was Hv1945, indicating a very high hardness. It was also found that cracks did not occur at the tip of the Vickers hardness test indentation and that the toughness was good. That is,
(A) is an SEM image. The part that appears white is the WC skeleton, and the part that appears black is the domain composed of the Fe—Mn solid solution phase. The metal domain inevitably grows during sintering, but it remains below 1 mm. The trace of the Vickers hardness test of this SEM image is shown. The Vickers hardness was Hv1945, indicating a very high hardness. It was also found that cracks did not occur at the tip of the Vickers hardness test indentation and that the toughness was good.
(B) is an X-ray image of W. The formation of the WC skeleton is shown. Further, a part of W is distributed in the Fe—Mn solid solution domain.
(C) shows the formation of a Fe—Mn solid solution domain which is an X-ray image of Fe.
(D) is an X-ray image of Co. It shows that a part of the binder phase Co is distributed to the Fe—Mn solid solution domains during sintering.
(E) is an X-ray image of C. The formation of the WC skeleton is shown.
(F) is an X-ray image of Mn. The formation of Fe-Mn solid solution domains is shown.
The reason why the WC carbide including the metal domain exhibits such a high hardness is that in the present invention, the WC skeleton has succeeded in creating a microstructure that restrains deformation of the metal domain.
　以上詳述したように、本発明合金粉末は、タングステン格子中に遷移金属元素を均一一様に強制固溶している。したがって、タングステンの一部を遷移金属元素で代替した合金粉末として、超硬合金用タングステン炭化物原料など、タングステンを省資源化するための用途に広く用いることができる。例えば、本発明のタングステン合金粉末はタングステン粉末と同様にタングステン炭化物を形成し、結合相Ｃｏで焼結した超硬合金を製造することができる。 As described in detail above, the alloy powder of the present invention has the transition metal element uniformly and uniformly dissolved in the tungsten lattice. Therefore, as an alloy powder in which a part of tungsten is replaced with a transition metal element, it can be widely used in applications for saving tungsten resources such as tungsten carbide raw material for cemented carbide. For example, the tungsten alloy powder of the present invention forms tungsten carbide in the same manner as the tungsten powder, and can produce a cemented carbide sintered with the binder phase Co.
試料Ｎｏ．２３の本発明材における金属相内包タングステン炭化物をＥＭＰＡ観察した結果を示す図である。（ａ）は、SEM像で、白く見える部分がＷＣ骨格であり、黒く見える部分が金属Ｃｏからなるドメインである。（ｂ）はＷのＸ線像で、ＷＣ骨格の形成を示す。（ｃ）はＣｏのＸ線像で、ＷＣ骨格中のＣｏドメインの形成を示す。（ｄ）はＣのＸ線像で、ＷＣ骨格の形成を示す。Sample No. It is a figure which shows the result of having observed the metal phase inclusion tungsten carbide in 23 material of this invention by EMPA. (A) is a SEM image, the white part is a WC skeleton, and the black part is a domain made of Co. (B) is an X-ray image of W and shows the formation of the WC skeleton. (C) is an X-ray image of Co, showing the formation of a Co domain in the WC skeleton. (D) is an X-ray image of C, showing the formation of a WC skeleton. 試料Ｎｏ．３４の本発明材における金属相内包タングステン炭化物をＥＭＰＡ観察した結果を示す図である。（ａ）は、SEM像で、白く見える部分がＷＣ骨格であり、黒く見える部分がＦｅ－Ｍｎ固溶体相からなるドメインである。（ｂ）は、ＷのＸ線像で、ＷＣ骨格の形成を示す。（ｃ）は、ＦｅのＸ線像で、Ｆｅ－Ｍｎ固溶体ドメインの形成を示す。（ｄ）は、Ｃｏのｘ線像で、結合相Ｃｏの一部は焼結中にＦｅ－Ｍｎ固溶体ドメインに分配されることを示す。（ｅ）は、ＣのＸ線像で、ＷＣ骨格の形成を示す。（ｆ）は、ＭｎのＸ線像で、Ｆｅ－Ｍｎ固溶体ドメインの形成を示す。Sample No. It is a figure which shows the result of having observed the metal phase inclusion tungsten carbide in 34 this invention materials by EMPA. (A) is an SEM image, the white portion is a WC skeleton, and the black portion is a domain composed of a Fe—Mn solid solution phase. (B) is an X-ray image of W and shows the formation of a WC skeleton. (C) is an X-ray image of Fe and shows the formation of a Fe—Mn solid solution domain. (D) is an x-ray image of Co and shows that a part of the binder phase Co is distributed to the Fe—Mn solid solution domain during sintering. (E) is an X-ray image of C and shows the formation of a WC skeleton. (F) is an X-ray image of Mn, showing the formation of Fe—Mn solid solution domains.

Claims (6)

  1. 　コバルト、鉄、マンガン及びニッケルの群から選ばれる少なくとも１種の遷移金属元素がタングステン格子中に固溶されてなり、Ｘ線回折図形にｂｃｃタングステン相ピークが認められる式［１］で示される遷移金属固溶タングステン合金粉末。
    　　　式［１］：Ｍ－Ｗ（但し、ＭはＣｏ、Ｆｅ、ＭｎまたはＮｉから選ばれる１種以上を示す）     Transition represented by the formula [1] in which at least one transition metal element selected from the group of cobalt, iron, manganese and nickel is dissolved in a tungsten lattice, and a bcc tungsten phase peak is observed in an X-ray diffraction pattern. Metal solute tungsten alloy powder.
    Formula [1]: MW (wherein M represents one or more selected from Co, Fe, Mn, or Ni)
  2. 　コバルトの一部を、鉄、マンガン及びニッケルの群から選ばれる１種以上と置換した
    式［２］：Ｃｏ－Ｍ１－Ｗ（但し、Ｍ１はＦｅ、ＭｎまたはＮｉから選ばれる１種以上を示す）で示される請求項１記載の遷移金属固溶タングステン合金粉末。     Formula [2]: Co-M1-W in which a part of cobalt is substituted with one or more selected from the group consisting of iron, manganese and nickel (where M1 represents one or more selected from Fe, Mn or Ni) The transition metal solid solution tungsten alloy powder of Claim 1 shown by this.
  3. 　鉄がタングステン格子中に固溶されてなり、鉄の一部がコバルト、マンガン及びニッケルの群から選ばれる１種以上と置換した
    　　　式［３］：Ｆｅ－Ｍ２－Ｗ（但し、Ｍ２は，Ｃｏ、ＭｎまたはＮｉから選ばれる１種以上を示す）で示される請求項１記載の遷移金属固溶タングステン合金粉末。     Iron is dissolved in a tungsten lattice, and a part of the iron is substituted with one or more selected from the group of cobalt, manganese, and nickel. Formula [3]: Fe—M2-W (where M2 is Co The transition metal solid solution tungsten alloy powder according to claim 1, wherein at least one selected from Mn and Ni is used.
  4. 　タングステン６０～９０ｍｏｌ％に対しコバルト、鉄、マンガン及びニッケルの群から選ばれる少なくとも１種４０～１０ｍｏｌ％を固溶させてなる請求項１～３のいずれかに記載の遷移金属固溶タングステン合金粉末。 4. The transition metal solid solution tungsten alloy powder according to claim 1, wherein at least one 40 to 10 mol% selected from the group consisting of cobalt, iron, manganese and nickel is dissolved in 60 to 90 mol% of tungsten. .
  5. 　タングステンイオンを含む水溶液と、コバルト、鉄、マンガン及びニッケルの群から選ばれる少なくとも１種の遷移金属イオンを含む水溶液を、タングステンイオンが６０ｍｏｌ％以上、遷移金属イオンが４０ｍｏｌ％以下の比率で混合し、
    　該混合水溶液を蒸発乾固させるか又は噴霧乾燥させ、
    　得られた固形物を酸化物に熱分解した後水素熱還元することによって、遷移金属元素を固溶した式［１］で示される遷移金属固溶タングステン合金粉末
    　　　式［１］：Ｍ－Ｗ（但し、ＭはＣｏ、Ｆｅ、ＭｎまたはＮｉから選ばれる１種以上を示す）
    を製造するようにしたことを特徴とする遷移金属固溶タングステン合金粉末の製造方法。     An aqueous solution containing tungsten ions and an aqueous solution containing at least one transition metal ion selected from the group consisting of cobalt, iron, manganese and nickel are mixed at a ratio of 60 mol% or more and 40 mol% or less of transition metal ions. ,
    Evaporating the mixed aqueous solution to dryness or spray drying;
    The obtained solid is thermally decomposed into oxides and then thermally reduced by hydrogen, so that the transition metal solid solution tungsten alloy powder represented by the formula [1] in which the transition metal element is dissolved is represented by the formula [1]: MW ( However, M shows 1 or more types chosen from Co, Fe, Mn, or Ni)
    A process for producing a transition metal solid solution tungsten alloy powder characterized by comprising producing
  6. 　タングステンイオンを含む水溶液がパラタングステン酸アンモニウム水溶液であり、コバルト、鉄、マンガン及びニッケルの群から選ばれる少なくとも一種の遷移金属イオンを含む水溶液が遷移金属錯体塩水溶液である請求項４記載の遷移金属固溶タングステン合金粉末の製造方法。 The transition metal according to claim 4, wherein the aqueous solution containing tungsten ions is an aqueous ammonium paratungstate solution, and the aqueous solution containing at least one transition metal ion selected from the group consisting of cobalt, iron, manganese and nickel is an aqueous transition metal complex salt solution. Manufacturing method of solid solution tungsten alloy powder.
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