WO2015064343A1 - Titanium alloy and artificial bone - Google Patents

Titanium alloy and artificial bone Download PDF

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WO2015064343A1
WO2015064343A1 PCT/JP2014/077190 JP2014077190W WO2015064343A1 WO 2015064343 A1 WO2015064343 A1 WO 2015064343A1 JP 2014077190 W JP2014077190 W JP 2014077190W WO 2015064343 A1 WO2015064343 A1 WO 2015064343A1
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modulus
alloy
young
titanium alloy
titanium
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PCT/JP2014/077190
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French (fr)
Japanese (ja)
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宮崎　修一
熙榮 金
和幸 菊地
直弥 根来
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国立大学法人筑波大学
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C14/00—Alloys based on titanium
    • A—HUMAN NECESSITIES
    • A61—MEDICAL OR VETERINARY SCIENCE; HYGIENE
    • A61L—METHODS OR APPARATUS FOR STERILISING MATERIALS OR OBJECTS IN GENERAL; DISINFECTION, STERILISATION OR DEODORISATION OF AIR; CHEMICAL ASPECTS OF BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES; MATERIALS FOR BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES
    • A61L27/00—Materials for grafts or prostheses or for coating grafts or prostheses
    • A61L27/02—Inorganic materials
    • A61L27/04—Metals or alloys
    • A61L27/06—Titanium or titanium alloys
    • A—HUMAN NECESSITIES
    • A61—MEDICAL OR VETERINARY SCIENCE; HYGIENE
    • A61L—METHODS OR APPARATUS FOR STERILISING MATERIALS OR OBJECTS IN GENERAL; DISINFECTION, STERILISATION OR DEODORISATION OF AIR; CHEMICAL ASPECTS OF BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES; MATERIALS FOR BANDAGES, DRESSINGS, ABSORBENT PADS OR SURGICAL ARTICLES
    • A61L2430/00—Materials or treatment for tissue regeneration
    • A61L2430/02—Materials or treatment for tissue regeneration for reconstruction of bones; weight-bearing implants

Definitions

  • the present invention relates to a titanium alloy and an artificial bone using the titanium alloy, and particularly to a titanium alloy and an artificial bone having a low Young's modulus and a high strength.
  • Titanium alloys are known to have good biocompatibility (rejection reaction etc. are difficult to occur even when used in a living body) and have been used as biomaterials.
  • a titanium alloy when used as an implant material in the treatment of a fracture site or the like, it is preferable to use a material close to bone characteristics (elastic modulus and strength). Since the elastic modulus (Young's modulus) of bone is about 10 to 40 [GPa], an alloy having a Young's modulus of 50 [GPa] or less is desired.
  • Patent Documents 1 to 10 For titanium alloys having a Young's modulus lower than that of pure titanium, techniques described in Patent Documents 1 to 10 below are known.
  • Japanese Patent No. 5143704 as Patent Document 1 contains 13 to 28 atom% (at%) of Nb and 0.1 to 10 at% of Sn, and any one of V, W, Zr and Al.
  • a Ti—Nb—Sn based alloy containing 0.1 to 5 at% of one kind is described.
  • the Ti—Nb—Sn alloy of Patent Document 1 has a Young's modulus measured by a resonance method of 54.2 GPa or more.
  • Patent Document 2 describes Ti— (25 wt% -40 wt%) Nb— (0-10 wt%) Sn alloy, Ti— (10 wt% —16 wt%) V— (0-8 wt%). ) A Sn alloy is described.
  • the Young's modulus measured by the resonance method is less than 50 [GPa] after 89% cold rolling, but it is 50 after heat treatment. [GPa] is exceeded. If it is only cold-rolled and not heat-treated, there is a problem that ductility is poor and uniform elongation is very small. Note that in a Ti—V—Sn titanium alloy, the Young's modulus measured by the resonance method is 59 [GPa] or more.
  • Patent Document 3 discloses a titanium alloy containing 13 to 28 atom% (at%) Nb and 0.1 to 10 at% Sn, or 13 to 28 atom% (at%). Ti—Nb—Sn containing 0.1 to 5 at% of any one or more of V, Mo, W, Zr and Al in addition to Nb of 0.1 to 10 to 10 at% of Sn Alloys are described. Each alloy of Patent Document 3 has a Young's modulus measured by a resonance method of 50.4 GPa or more.
  • Japanese Patent No. 4152050 as Patent Document 4 25-50 mass% (wt%) Ti, 25-60 mass% Zr, 10-20 mass% Nb, and 5-40 mass% Ta, Zr / Ta is 0.5 to 1.5, Nb / Ta is 0.125 to 1.5, tensile strength / Young's modulus is 0.016 or more, and Young's modulus is 70 GPa.
  • the following titanium alloys are described. In the titanium alloy described in Patent Document 4, the Young's modulus measured using an Instron tensile tester is 53.0 [GPa] or more.
  • Patent Document 5 contains 10.5 to 25% by mass (wt%) of Nb and 0.1 to 8% by mass of Sn. Containing at least one kind of Mo% by mass, 0.1-6.4% by mass Cr, 0.1-4.7% by mass Mn, and 0.1-3.2% by mass Fe
  • a titanium alloy in which molybdenum equivalents of Mo, Cr, Mn, and Fe are 2 to 8 and (mass% of Nb / 3.5) + (molybdenum equivalent) is 9 to 11 is described.
  • the Young's modulus measured by the resonance method is 67.1 [GPa] or more.
  • Japanese Patent No. 3375083 as Patent Document 6 describes a titanium alloy containing 30 to 60% by mass (wt%) of a Va group element (V, Nb, Ta).
  • the average Young's modulus is measured from a stress-strain diagram measured by an Instron tensile tester, and the average Young's modulus is 46 [GPa] or more.
  • the average Young's modulus is an index different from the general Young's modulus as described in paragraph No. “0006” of Patent Document 4, and is a lower value than the general Young's modulus. Therefore, it is unlikely that the general Young's modulus of the titanium alloy described in Patent Document 6 is 50 [GPa] or less even if the sweetness is estimated.
  • Patent Document 7 describes a titanium alloy containing 10 to 35 mass% (wt%) of Zr and 8 to 14 mass% of Cr.
  • the Young's modulus measured by the resonance method is 72 [GPa] or more.
  • Patent Document 8 contains 0.3 to 3% by mass (wt%) of one or more of oxygen, nitrogen and carbon and 1.8% by mass or less of Al.
  • a titanium alloy having a value obtained by subtracting the mass% of Al from the molybdenum equivalent of Mo, V, W, Nb, Ta, Fe, Cr, Ni, Co, and Cu is 3 to 11 mass% is described. Yes.
  • the Young's modulus derived from the stress-strain diagram is 50 [GPa] or more.
  • Patent Document 9 describes 3.5 to 7.0 mass% (wt%) Al, 1.4 to 3.6 mass% Fe, and 2.0 to 10 mass%. And a titanium alloy containing 0.0% by mass of Mo and having a molybdenum equivalent weight of 6.0 to 14.0% by mass. In the titanium alloy described in Patent Document 9, the Young's modulus measured by the resonance method is 65 [GPa] or more.
  • Patent Document 10 describes 12 to 30 wt% (wt%) of Nb, 12 to 30 wt% of Zr, 1 to 6 wt% of Al, and 1 to 8 wt%. Titanium alloys containing 1% Cr and 1-8% by weight Sn are described. In the titanium alloy described in Patent Document 10, the Young's modulus measured based on JIS using a tensile tester is 80 [GPa] or more.
  • Japanese Patent No. 5143704 ("0026") Japanese Patent No. 5005889 (“0032” to “0042”, FIG. 2) JP 2005-113227 A (“0026” to “0027”) Japanese Patent No. 4152050 (“0049”, “0053”) JP 2010-1503 (“0028” to “0030") Japanese Patent No. 3375083 ("0114” to “0122”) JP 2004-353039 A (“0013” to “0015”) JP 2004-162171 A (“0045” to “0051”) JP 2010-216011 (“0030” to “0032”) JP 2008-101234 A (“0037”, FIG. 1)
  • the technical problem of the present invention is to provide a titanium alloy having a low Young's modulus and a high strength.
  • the titanium alloy of the invention according to claim 1 1 to 15 at% niobium, 2at% or more and 5at% or less of iron, Aluminum of 2 at% or more and 12 at% or less, The remaining titanium, With inevitable impurities, It is characterized by comprising.
  • a titanium alloy according to claim 1 is used.
  • the first and second aspects of the invention it is possible to provide a titanium alloy having a low Young's modulus and a high strength as compared with the conventional configuration.
  • iron and aluminum since iron and aluminum are used, raw material costs can be reduced and the melting point can be lowered as compared with the case of using rare metals.
  • FIG. 1 shows the results of evaluating changes in the properties of the alloy when the concentration of aluminum is changed.
  • FIG. 1A is a graph in which the horizontal axis indicates the aluminum content and the vertical axis indicates the Young's modulus.
  • FIG. It is the graph which took the content of aluminum on the axis
  • FIG. 2 is an explanatory diagram comparing the concentration dependence of aluminum, and is a graph of stress-strain curves of alloys 5, 17 and 19, with the horizontal axis representing strain and the vertical axis representing stress. .
  • FIG. 3 is a result of evaluating the change in the characteristics of the alloy when the iron concentration is changed.
  • FIG. 1A is a graph in which the horizontal axis indicates the aluminum content and the vertical axis indicates the Young's modulus.
  • FIG. It is the graph which took the content of aluminum on the axis
  • FIG. 2 is an explanatory diagram
  • FIG. 3A is a graph in which the horizontal axis indicates the iron content and the vertical axis indicates the Young's modulus.
  • FIG. It is the graph which took iron content on the axis
  • FIG. 4 is an explanatory diagram comparing the concentration dependence of iron, and is a graph of stress-strain curves of alloys 5, 15, and 23, with the horizontal axis representing strain and the vertical axis representing stress. .
  • FIG. 5 is an explanatory diagram for comparison between the existing alloy and the alloy of the example, and is a graph in which Young's modulus is taken on the horizontal axis and tensile strength is taken on the vertical axis.
  • Test specimens of Alloy 1 to Alloy 13 having the alloy compositions shown in Table 1 below, which are examples of the present invention, and Alloy 14 to Alloy 24 as comparative examples were prepared and tested.
  • the test pieces used in the experiment were produced by the following methods (1) to (3).
  • (1) At% of each metal element is measured and melted by an arc melting method to produce an alloy ingot. That is, Alloy 1 (Ti-13Nb-2Fe-4Al) is an alloy having an alloy composition of 13 at% Nb, 2 at% Fe, 4 at% Al, and the balance (81 at%) of Ti.
  • Ti-7Nb-3Fe-2Al is an alloy having an alloy composition of 7 at% Nb, 3 at% Fe, 2 at% Al, and the balance (88 at%) of Ti.
  • the produced alloy ingot is cold-rolled at a rolling rate of 80% to 95% with a cold rolling mill to produce a plate material.
  • a test specimen for measurement is cut out from the plate material by an electric discharge machine.
  • the test piece for measuring Young's modulus has a length of 30 mm, a width of 6 mm, and a thickness of 0.2 mm.
  • the specimen for the tensile test has a gauge length of 20 mm, a width of 1.5 mm, and a thickness of 0.2 mm.
  • the cut specimen is subjected to heat treatment at 900 ° C. for 30 minutes in an argon atmosphere.
  • the quaternary alloy with Nb of 1 to 15 at%, Fe of 2 to 5 at%, and Al of 2 to 12 at% has a Young's modulus of less than 50 [GPa] and a maximum stress of 600 [MPa] or more.
  • Alloys 5 to 10 and 13 have a Young's modulus of 30 [GPa], close to the Young's modulus of human bone, and can be suitably used as a material for artificial bones.
  • the Young's modulus and the maximum stress cannot be measured, and the cold workability is very bad.
  • there is more niobium than 16 at% as shown in the alloy 14, there is a problem that the maximum stress (strength) becomes low and the Young's modulus exceeds 50 [GPa].
  • FIG. 1 shows the results of evaluating changes in the properties of the alloy when the concentration of aluminum is changed.
  • FIG. 1A is a graph in which the horizontal axis indicates the aluminum content and the vertical axis indicates the Young's modulus.
  • FIG. It is the graph which took the content of aluminum on the axis
  • FIG. 2 is an explanatory diagram comparing the concentration dependence of aluminum, and is a graph of stress-strain curves of alloys 5, 17 and 19, with the horizontal axis representing strain and the vertical axis representing stress. .
  • FIG. 1A is a graph in which the horizontal axis indicates the aluminum content and the vertical axis indicates the Young's modulus.
  • FIG. It is the graph which took the content of aluminum on the axis
  • FIG. 2 is an explanatory diagram comparing the concentration dependence of aluminum, and is a graph of stress-strain curves
  • FIG. 3 is a result of evaluating the change in the characteristics of the alloy when the iron concentration is changed.
  • FIG. 3A is a graph in which the horizontal axis indicates the iron content and the vertical axis indicates the Young's modulus.
  • FIG. It is the graph which took iron content on the axis
  • FIG. 4 is an explanatory diagram comparing the concentration dependence of iron, and is a graph of stress-strain curves of alloys 5, 15, and 23, with the horizontal axis representing strain and the vertical axis representing stress. .
  • FIG. 3A is a graph in which the horizontal axis indicates the iron content and the vertical axis indicates the Young's modulus.
  • FIG. It is the graph which took iron content on the axis
  • FIG. 4 is an explanatory diagram comparing the concentration dependence of iron, and is a graph of stress-strain curves of alloys
  • FIG. 5 is an explanatory diagram for comparison between the existing alloy and the alloy of the example, and is a graph in which Young's modulus is taken on the horizontal axis and tensile strength is taken on the vertical axis. Therefore, in the alloys of Examples, Patent Documents 1 to 10 are made of titanium alloys containing 1 at% or more and 5 at% or less of niobium, 2 at% or more and 5 at% or less of iron, and 2 at% or more and 12 at% or less of aluminum. Compared with the alloy shown in FIG. 1, an alloy having a Young's modulus of less than 50 [GPa] and a strength of 600 [MPa] or more and good workability can be provided. As shown in FIG.
  • the strength increases as the Young's modulus increases, and the strength tends to decrease as the Young's modulus decreases.
  • the alloy of the example can realize a high strength titanium alloy while realizing a low Young's modulus of less than 50 [GPa]. Therefore, a titanium alloy having a low Young's modulus, high strength, good workability, and high biocompatibility can be provided.
  • Nb is 15 at% or less, and since relatively inexpensive elements such as Fe and Al are used, so-called rare metals such as V, Zr, Mo, and W are used. Compared to conventional alloys, the manufacturing cost can also be reduced.
  • titanium alloys other than Ti—Ni alloys have a high melting point, and there is a problem that a large-scale facility is required for melting, manufacturing and processing.
  • Fe and Al are added, the melting point of the alloy tends to be lowered. Therefore, it is possible to manufacture without increasing the temperature, and it can be expected to reduce the manufacturing cost.
  • Example of this invention was explained in full detail, this invention is not limited to the said Example, A various change is performed within the range of the summary of this invention described in the claim. It is possible. For example, using high biocompatibility, it can be suitably used for a living body / medical member used in an operation or treatment such as an artificial bone, an implant, or an orthodontic wire, but is not limited thereto. For example, using low Young's modulus (high flexibility) and high strength, it can be suitably applied to glasses frames, golf clubs, automobiles such as suspensions and springs, motorcycle parts, and leisure goods such as tent poles. It is.

Abstract

Provided is a titanium alloy which is characterized by being composed of from 1 at% to 15 at% (inclusive) of niobium, from 2 at% to 5 at% (inclusive) of iron, from 2 at% to 12 at% (inclusive) of aluminum with the balance made up of titanium and unavoidable impurities. This titanium alloy has low Young's modulus and high strength.

Description

チタン合金および人工骨Titanium alloy and artificial bone
　本発明は、チタン合金および前記チタン合金が使用された人工骨に関し、特に、低ヤング率で高強度のチタン合金および人工骨に関する。 The present invention relates to a titanium alloy and an artificial bone using the titanium alloy, and particularly to a titanium alloy and an artificial bone having a low Young's modulus and a high strength.
　チタン合金は、生体適合性がよい（生体に使用しても拒絶反応等がでにくい）ことが知られており、従来から生体材料として使用されてきた。特に、骨折の部位の治療等において、インプラント材としてチタン合金を使用する場合には、骨の特性（弾性率や強度）に近い材料を使用することが好ましい。骨の弾性率（ヤング率）は、１０～４０［ＧＰａ］程度であるため、ヤング率が５０［ＧＰａ］以下の合金が望まれている。 Titanium alloys are known to have good biocompatibility (rejection reaction etc. are difficult to occur even when used in a living body) and have been used as biomaterials. In particular, when a titanium alloy is used as an implant material in the treatment of a fracture site or the like, it is preferable to use a material close to bone characteristics (elastic modulus and strength). Since the elastic modulus (Young's modulus) of bone is about 10 to 40 [GPa], an alloy having a Young's modulus of 50 [GPa] or less is desired.
　ヤング率が純チタンよりも低くしたチタン合金について、下記の特許文献１～１０に記載の技術が公知である。
　特許文献１としての特許第５１４３７０４号公報には、１３～２８ａｔｏｍ％（ａｔ％）のＮｂと０．１～１０ａｔ％のＳｎとを含有し、さらに、Ｖ，Ｗ，ＺｒおよびＡｌのうちのいずれか１種を０．１～５ａｔ％含有するＴｉ－Ｎｂ－Ｓｎ系合金が記載されている。特許文献１のＴｉ－Ｎｂ－Ｓｎ合金は、共振法で測定されたヤング率が、５４．２ＧＰａ以上となっている。 For titanium alloys having a Young's modulus lower than that of pure titanium, techniques described in Patent Documents 1 to 10 below are known.
Japanese Patent No. 5143704 as Patent Document 1 contains 13 to 28 atom% (at%) of Nb and 0.1 to 10 at% of Sn, and any one of V, W, Zr and Al. A Ti—Nb—Sn based alloy containing 0.1 to 5 at% of one kind is described. The Ti—Nb—Sn alloy of Patent Document 1 has a Young's modulus measured by a resonance method of 54.2 GPa or more.
　特許文献２としての特許第５００５８８９号公報には、Ｔｉ－（２５ｗｔ％－４０ｗｔ％）Ｎｂ－（０－１０ｗｔ％）Ｓｎ合金や、Ｔｉ－（１０ｗｔ％－１６ｗｔ％）Ｖ－（０－８ｗｔ％）Ｓｎ合金が記載されている。特許文献２のＴｉ－Ｎｂ－Ｓｎ系のチタン合金では、共振法で測定されたヤング率が、８９％冷間圧延後は５０［ＧＰａ］未満となっているが、熱処理を行った後は５０［ＧＰａ］を超えている。冷間圧延しただけで、熱処理をしないと、延性に乏しく均一伸びが非常に小さい問題がある。なお、Ｔｉ－Ｖ－Ｓｎ系のチタン合金では、共振法で測定されたヤング率は、５９［ＧＰａ］以上となっている。 Japanese Patent No. 5005889 as Patent Document 2 describes Ti— (25 wt% -40 wt%) Nb— (0-10 wt%) Sn alloy, Ti— (10 wt% —16 wt%) V— (0-8 wt%). ) A Sn alloy is described. In the Ti—Nb—Sn titanium alloy of Patent Document 2, the Young's modulus measured by the resonance method is less than 50 [GPa] after 89% cold rolling, but it is 50 after heat treatment. [GPa] is exceeded. If it is only cold-rolled and not heat-treated, there is a problem that ductility is poor and uniform elongation is very small. Note that in a Ti—V—Sn titanium alloy, the Young's modulus measured by the resonance method is 59 [GPa] or more.
　特許文献３としての特開２００５－１１３２２７号公報には、１３～２８ａｔｏｍ％（ａｔ％）のＮｂと０．１～１０ａｔ％のＳｎとを含有するチタン合金や、１３～２８ａｔｏｍ％（ａｔ％）のＮｂと０．１～１０ａｔ％のＳｎとに加え、Ｖ，Ｍｏ，Ｗ，ＺｒおよびＡｌのうちのいずれか１種または２種以上を０．１～５ａｔ％含有するＴｉ－Ｎｂ－Ｓｎ系合金が記載されている。特許文献３の各合金は、共振法で測定されたヤング率が、５０．４ＧＰａ以上となっている。 Japanese Patent Laid-Open No. 2005-113227 as Patent Document 3 discloses a titanium alloy containing 13 to 28 atom% (at%) Nb and 0.1 to 10 at% Sn, or 13 to 28 atom% (at%). Ti—Nb—Sn containing 0.1 to 5 at% of any one or more of V, Mo, W, Zr and Al in addition to Nb of 0.1 to 10 to 10 at% of Sn Alloys are described. Each alloy of Patent Document 3 has a Young's modulus measured by a resonance method of 50.4 GPa or more.
　特許文献４としての特許第４１５２０５０号公報には、２５～５０質量％（ｗｔ％）のＴｉと、２５～６０質量％のＺｒと、１０～２０質量％のＮｂと、５～４０質量％のＴａと、を含有し、Ｚｒ／Ｔａが０．５～１．５であり、且つ、Ｎｂ／Ｔａが０．１２５～１．５、引っ張り強度／ヤング率が０．０１６以上、ヤング率が７０ＧＰａ以下のチタン合金が記載されている。特許文献４に記載のチタン合金では、インストロン引張り試験機を使用して測定されたヤング率が５３．０［ＧＰａ］以上となっている。 In Japanese Patent No. 4152050 as Patent Document 4, 25-50 mass% (wt%) Ti, 25-60 mass% Zr, 10-20 mass% Nb, and 5-40 mass% Ta, Zr / Ta is 0.5 to 1.5, Nb / Ta is 0.125 to 1.5, tensile strength / Young's modulus is 0.016 or more, and Young's modulus is 70 GPa. The following titanium alloys are described. In the titanium alloy described in Patent Document 4, the Young's modulus measured using an Instron tensile tester is 53.0 [GPa] or more.
　特許文献５としての特開２０１０－１５０３号公報には、１０．５～２５質量％（ｗｔ％）のＮｂと、０．１～８質量％のＳｎと、を含有し、０．１～８質量％のＭｏと、０．１～６．４質量％のＣｒと、０．１～４．７質量％のＭｎと、０．１～３．２質量％のＦｅと、を少なくとも１種類含有し、Ｍｏ、Ｃｒ、Ｍｎ、Ｆｅのモリブデン当量が２～８、且つ、（Ｎｂの質量％／３．５）＋（モリブデン当量）が９～１１であるチタン合金が記載されている。特許文献５に記載のチタン合金では、共振法により測定されたヤング率は、６７．１［ＧＰａ］以上となっている。 Japanese Patent Application Laid-Open No. 2010-1503 as Patent Document 5 contains 10.5 to 25% by mass (wt%) of Nb and 0.1 to 8% by mass of Sn. Containing at least one kind of Mo% by mass, 0.1-6.4% by mass Cr, 0.1-4.7% by mass Mn, and 0.1-3.2% by mass Fe In addition, a titanium alloy in which molybdenum equivalents of Mo, Cr, Mn, and Fe are 2 to 8 and (mass% of Nb / 3.5) + (molybdenum equivalent) is 9 to 11 is described. In the titanium alloy described in Patent Document 5, the Young's modulus measured by the resonance method is 67.1 [GPa] or more.
　特許文献６としての特許第３３７５０８３号公報には、３０～６０質量％（ｗｔ％）のＶａ族元素（Ｖ，Ｎｂ，Ｔａ）と、を含有するチタン合金が記載されている。特許文献６に記載のチタン合金では、インストロン引張り試験機により測定された応力－歪み線図から、平均ヤング率を測定しており、平均ヤング率が４６［ＧＰａ］以上となっている。なお、平均ヤング率に関しては、特許文献４の段落番号「０００６」に記載されているように、一般のヤング率とは異なる指標であり、一般のヤング率に比べて、低い値となる。したがって、特許文献６に記載されたチタン合金における一般のヤング率は、甘めに見積もっても５０［ＧＰａ］以下を実現しているとは考えにくい。 Japanese Patent No. 3375083 as Patent Document 6 describes a titanium alloy containing 30 to 60% by mass (wt%) of a Va group element (V, Nb, Ta). In the titanium alloy described in Patent Document 6, the average Young's modulus is measured from a stress-strain diagram measured by an Instron tensile tester, and the average Young's modulus is 46 [GPa] or more. The average Young's modulus is an index different from the general Young's modulus as described in paragraph No. “0006” of Patent Document 4, and is a lower value than the general Young's modulus. Therefore, it is unlikely that the general Young's modulus of the titanium alloy described in Patent Document 6 is 50 [GPa] or less even if the sweetness is estimated.
　特許文献７としての特開２００４－３５３０３９号公報には、１０～３５質量％（ｗｔ％）のＺｒと、８～１４質量％のＣｒと、を含有するチタン合金が記載されている。特許文献７に記載のチタン合金では、共振法により測定されたヤング率は、７２［ＧＰａ］以上となっている。 Japanese Patent Application Laid-Open No. 2004-353039 as Patent Document 7 describes a titanium alloy containing 10 to 35 mass% (wt%) of Zr and 8 to 14 mass% of Cr. In the titanium alloy described in Patent Document 7, the Young's modulus measured by the resonance method is 72 [GPa] or more.
　特許文献８としての特開２００４－１６２１７１号公報には、０．３～３質量％（ｗｔ％）の酸素、窒素、炭素の１種類以上と、１．８質量％以下のＡｌと、を含有するチタン合金において、Ｍｏ、Ｖ、Ｗ、Ｎｂ、Ｔａ、Ｆｅ、Ｃｒ、Ｎｉ、Ｃｏ、Ｃｕのモリブデン当量からＡｌの質量％を減算した値が３～１１質量％であるチタン合金が記載されている。特許文献８に記載のチタン合金では、応力－歪み線図から導出されたヤング率は、５０［ＧＰａ］以上となっている。 Japanese Patent Application Laid-Open No. 2004-162171 as Patent Document 8 contains 0.3 to 3% by mass (wt%) of one or more of oxygen, nitrogen and carbon and 1.8% by mass or less of Al. In the titanium alloy, a titanium alloy having a value obtained by subtracting the mass% of Al from the molybdenum equivalent of Mo, V, W, Nb, Ta, Fe, Cr, Ni, Co, and Cu is 3 to 11 mass% is described. Yes. In the titanium alloy described in Patent Document 8, the Young's modulus derived from the stress-strain diagram is 50 [GPa] or more.
　特許文献９としての特開２０１０－２１６０１１号公報には、３．５～７．０質量％（ｗｔ％）のＡｌと、１．４～３．６質量％のＦｅと、２．０～１０．０質量％のＭｏと、を含有し、モリブデン当量が６．０～１４．０質量％であるチタン合金が記載されている。特許文献９に記載のチタン合金では、共振法により測定されたヤング率は、６５［ＧＰａ］以上となっている。 Japanese Patent Application Laid-Open No. 2010-216011 as Patent Document 9 describes 3.5 to 7.0 mass% (wt%) Al, 1.4 to 3.6 mass% Fe, and 2.0 to 10 mass%. And a titanium alloy containing 0.0% by mass of Mo and having a molybdenum equivalent weight of 6.0 to 14.0% by mass. In the titanium alloy described in Patent Document 9, the Young's modulus measured by the resonance method is 65 [GPa] or more.
　特許文献１０としての特開２００８－１０１２３４号公報には、１２～３０重量％（ｗｔ％）のＮｂと、１２～３０重量％のＺｒと、１～６重量％のＡｌと、１～８重量％のＣｒと、１～８重量％のＳｎと、を含有するチタン合金が記載されている。特許文献１０に記載のチタン合金では、引張り試験機を使用してＪＩＳに基づいて測定されたヤング率は、８０［ＧＰａ］以上となっている。 Japanese Patent Application Laid-Open No. 2008-101234 as Patent Document 10 describes 12 to 30 wt% (wt%) of Nb, 12 to 30 wt% of Zr, 1 to 6 wt% of Al, and 1 to 8 wt%. Titanium alloys containing 1% Cr and 1-8% by weight Sn are described. In the titanium alloy described in Patent Document 10, the Young's modulus measured based on JIS using a tensile tester is 80 [GPa] or more.
特許第５１４３７０４号公報（「００２６」）Japanese Patent No. 5143704 ("0026") 特許第５００５８８９号公報（「００３２」～「００４２」、図２）Japanese Patent No. 5005889 (“0032” to “0042”, FIG. 2) 特開２００５－１１３２２７号公報（「００２６」～「００２７」）JP 2005-113227 A (“0026” to “0027”) 特許第４１５２０５０号公報（「００４９」、「００５３」）Japanese Patent No. 4152050 (“0049”, “0053”) 特開２０１０－１５０３号公報（「００２８」～「００３０」）JP 2010-1503 ("0028" to "0030") 特許第３３７５０８３号公報（「０１１４」～「０１２２」）Japanese Patent No. 3375083 ("0114" to "0122") 特開２００４－３５３０３９号公報（「００１３」～「００１５」）JP 2004-353039 A (“0013” to “0015”) 特開２００４－１６２１７１号公報（「００４５」～「００５１」）JP 2004-162171 A (“0045” to “0051”) 特開２０１０－２１６０１１号公報（「００３０」～「００３２」）JP 2010-216011 (“0030” to “0032”) 特開２００８－１０１２３４号公報（「００３７」、図１）JP 2008-101234 A (“0037”, FIG. 1)
（従来技術の問題点）
　前述のように、従来のチタン合金では、５０［ＧＰａ］未満のものはほとんど存在せず、骨のヤング率に近い２０～４０［ＧＰａ］のチタン合金は得られていない。骨のインプラントとして、骨よりもヤング率の高い材料を使用した場合、荷重が骨にかからず、インプラントにかかってしまい、かえって骨が弱くなってしまう問題がある。
　また、従来の低ヤング率チタン合金はＺｒ、Ｔａなど高価で重いレアメタルを多く含んでいる。
　一方で、一般的に、合金では、ヤング率を低くすると、引っ張り強度も低下する傾向にあり、強度が低下すると、永久歪みが入り易く耐久性に乏しい。 (Problems of conventional technology)
As described above, there are almost no conventional titanium alloys having a value of less than 50 [GPa], and no titanium alloy having 20 to 40 [GPa] close to the Young's modulus of bone has been obtained. When a material having a higher Young's modulus than bone is used as a bone implant, there is a problem that the load is not applied to the bone but applied to the implant, and the bone is weakened.
Further, the conventional low Young's modulus titanium alloy contains a lot of expensive and heavy rare metals such as Zr and Ta.
On the other hand, in general, when the Young's modulus is lowered, the tensile strength tends to be lowered in the alloy, and when the strength is lowered, permanent deformation is likely to occur and the durability is poor.
　本発明は、低ヤング率で高強度のチタン合金を提供することを技術的課題とする。 The technical problem of the present invention is to provide a titanium alloy having a low Young's modulus and a high strength.
　前記技術的課題を解決するために、請求項１に記載の発明のチタン合金は、
　１ａｔ％以上１５ａｔ％以下のニオブと、
　２ａｔ％以上５ａｔ％以下の鉄と、
　２ａｔ％以上１２ａｔ％以下のアルミニウムと、
　残部のチタンと、
　不可避的不純物と、
　からなることを特徴とする。 In order to solve the technical problem, the titanium alloy of the invention according to claim 1,
1 to 15 at% niobium,
2at% or more and 5at% or less of iron,
Aluminum of 2 at% or more and 12 at% or less,
The remaining titanium,
With inevitable impurities,
It is characterized by comprising.
　前記技術的課題を解決するために、請求項２に記載の発明の人工骨は、
　請求項１に記載のチタン合金により構成されたことを特徴とする。 In order to solve the technical problem, the artificial bone of the invention according to claim 2,
A titanium alloy according to claim 1 is used.
　請求項１、２に記載の発明によれば、従来の構成に比べて、低ヤング率で高強度のチタン合金を提供することができる。また、鉄とアルミニウムを使用しており、レアメタルを使用する場合に比べて、原材料費を低減できると共に、融点を低下させることができる。 According to the first and second aspects of the invention, it is possible to provide a titanium alloy having a low Young's modulus and a high strength as compared with the conventional configuration. In addition, since iron and aluminum are used, raw material costs can be reduced and the melting point can be lowered as compared with the case of using rare metals.
図１はアルミニウムの濃度を変化させた場合の合金の特性の変化を評価した結果であり、図１Ａは横軸にアルミニウムの含有量を取り縦軸にヤング率を取ったグラフ、図１Ｂは横軸にアルミニウムの含有量を取り縦軸に最大応力を取ったグラフである。FIG. 1 shows the results of evaluating changes in the properties of the alloy when the concentration of aluminum is changed. FIG. 1A is a graph in which the horizontal axis indicates the aluminum content and the vertical axis indicates the Young's modulus. FIG. It is the graph which took the content of aluminum on the axis | shaft, and took the maximum stress on the ordinate. 図２はアルミニウムの濃度依存性を対比する説明図であり、合金５，１７，１９の応力－歪み曲線のグラフであって、横軸にひずみを取り、縦軸に応力を取ったグラフである。FIG. 2 is an explanatory diagram comparing the concentration dependence of aluminum, and is a graph of stress-strain curves of alloys 5, 17 and 19, with the horizontal axis representing strain and the vertical axis representing stress. . 図３は鉄の濃度を変化させた場合の合金の特性の変化を評価した結果であり、図３Ａは横軸に鉄の含有量を取り縦軸にヤング率を取ったグラフ、図３Ｂは横軸に鉄の含有量を取り縦軸に最大応力を取ったグラフである。FIG. 3 is a result of evaluating the change in the characteristics of the alloy when the iron concentration is changed. FIG. 3A is a graph in which the horizontal axis indicates the iron content and the vertical axis indicates the Young's modulus. FIG. It is the graph which took iron content on the axis | shaft and took the maximum stress on the vertical axis | shaft. 図４は鉄の濃度依存性を対比する説明図であり、合金５，１５，２３の応力－歪み曲線のグラフであって、横軸にひずみを取り、縦軸に応力を取ったグラフである。FIG. 4 is an explanatory diagram comparing the concentration dependence of iron, and is a graph of stress-strain curves of alloys 5, 15, and 23, with the horizontal axis representing strain and the vertical axis representing stress. . 図５は既存の合金と実施例の合金との対比説明図であり、横軸にヤング率を取り縦軸に引っ張り強さを取ったグラフである。FIG. 5 is an explanatory diagram for comparison between the existing alloy and the alloy of the example, and is a graph in which Young's modulus is taken on the horizontal axis and tensile strength is taken on the vertical axis.
　次に実施例を使用して、本発明を詳細に説明する。 Next, the present invention will be described in detail using examples.
　本発明の実施例である下記表１に示す合金組成の合金１～合金１３および比較例としての合金１４～合金２４の試験片を作製して、実験を行った。実験に使用した試験片は、下記の方法（１）～（３）により作製された。
（１）各金属元素のａｔ％を計測してアーク溶解法により溶融して合金インゴットを作製する。すなわち、合金１（Ｔｉ－１３Ｎｂ－２Ｆｅ－４Ａｌ）は、１３ａｔ％のＮｂと、２ａｔ％のＦｅと、４ａｔ％のＡｌと、残部（８１ａｔ％）のＴｉの合金組成の合金であり、合金２（Ｔｉ－７Ｎｂ－３Ｆｅ－２Ａｌ）は７ａｔ％のＮｂと、３ａｔ％のＦｅと、２ａｔ％のＡｌと、残部（８８ａｔ％）のＴｉの合金組成の合金である。
（２）作成された合金インゴットを冷間圧延機で８０％～９５％の圧延率で冷間圧延して、板材を作製する。
（３）板材から測定用の試験片を放電加工機により切り出す。ヤング率測定用の試験片は長さ３０ｍｍ、幅６ｍｍ、厚さ０．２ｍｍである。引張試験の試験片はゲージ長２０ｍｍ、幅１．５ｍｍ、厚さ０．２ｍｍである。
（４）切り出した試験片に、アルゴン雰囲気で９００℃、３０分の熱処理を施す。 Test specimens of Alloy 1 to Alloy 13 having the alloy compositions shown in Table 1 below, which are examples of the present invention, and Alloy 14 to Alloy 24 as comparative examples were prepared and tested. The test pieces used in the experiment were produced by the following methods (1) to (3).
(1) At% of each metal element is measured and melted by an arc melting method to produce an alloy ingot. That is, Alloy 1 (Ti-13Nb-2Fe-4Al) is an alloy having an alloy composition of 13 at% Nb, 2 at% Fe, 4 at% Al, and the balance (81 at%) of Ti. (Ti-7Nb-3Fe-2Al) is an alloy having an alloy composition of 7 at% Nb, 3 at% Fe, 2 at% Al, and the balance (88 at%) of Ti.
(2) The produced alloy ingot is cold-rolled at a rolling rate of 80% to 95% with a cold rolling mill to produce a plate material.
(3) A test specimen for measurement is cut out from the plate material by an electric discharge machine. The test piece for measuring Young's modulus has a length of 30 mm, a width of 6 mm, and a thickness of 0.2 mm. The specimen for the tensile test has a gauge length of 20 mm, a width of 1.5 mm, and a thickness of 0.2 mm.
(4) The cut specimen is subjected to heat treatment at 900 ° C. for 30 minutes in an argon atmosphere.
（合金特性の測定試験）
　前記作製方法で作製された合金のヤング率は片持ち共振法により、最大強度は引張試験により測定した。冷間圧延機で８０％の圧延が出来ず、試験片が得られなかった場合には、「－」で表記した。
　また、９５％冷間圧延が可能な場合は加工性が良好な「○」、９５％冷間圧延が不能であったが９０％冷間圧延が可能な場合は「△」、９０％冷間圧延が不能な場合は「×」と評価した。
　結果を表１に示す。 (Measurement test of alloy properties)
The Young's modulus of the alloy produced by the production method was measured by a cantilever resonance method, and the maximum strength was measured by a tensile test. When 80% rolling was not possible with a cold rolling mill and a test piece was not obtained, it was indicated by “−”.
Also, when 95% cold rolling is possible, good workability is “◯”, and when 95% cold rolling is impossible, 90% cold rolling is possible, “△”, 90% cold When rolling was impossible, it evaluated as "x".
The results are shown in Table 1.
Figure JPOXMLDOC01-appb-T000001
Figure JPOXMLDOC01-appb-T000001
　前記実験結果から、Ｎｂが１～１５ａｔ％、Ｆｅが２～５ａｔ％、Ａｌが２～１２ａｔ％の四元合金では、ヤング率が５０［ＧＰａ］未満且つ、最大応力が６００［ＭＰａ］以上であると共に、少なくとも９０％冷間加工性が可能な良好な加工性を有することが確認された。特に、合金５～１０、１３は、ヤング率が３０［ＧＰａ］台を実現しており、人間の骨のヤング率に近く、人工骨の材料として好適に使用可能である。
　前記実験結果から、ニオブが添加されない場合、合金２４に示すように、ヤング率や最大応力が測定できず、冷間加工性が非常に悪い問題がある。一方で、ニオブが１６ａｔ％より多い場合、合金１４に示すように、最大応力（強度）が低くなり、ヤング率が５０［ＧＰａ］を超える問題がある。 From the above experimental results, the quaternary alloy with Nb of 1 to 15 at%, Fe of 2 to 5 at%, and Al of 2 to 12 at% has a Young's modulus of less than 50 [GPa] and a maximum stress of 600 [MPa] or more. In addition, it was confirmed that it has good workability capable of at least 90% cold workability. In particular, Alloys 5 to 10 and 13 have a Young's modulus of 30 [GPa], close to the Young's modulus of human bone, and can be suitably used as a material for artificial bones.
From the above experimental results, when niobium is not added, as shown in the alloy 24, the Young's modulus and the maximum stress cannot be measured, and the cold workability is very bad. On the other hand, when there is more niobium than 16 at%, as shown in the alloy 14, there is a problem that the maximum stress (strength) becomes low and the Young's modulus exceeds 50 [GPa].
　図１はアルミニウムの濃度を変化させた場合の合金の特性の変化を評価した結果であり、図１Ａは横軸にアルミニウムの含有量を取り縦軸にヤング率を取ったグラフ、図１Ｂは横軸にアルミニウムの含有量を取り縦軸に最大応力を取ったグラフである。
　図２はアルミニウムの濃度依存性を対比する説明図であり、合金５，１７，１９の応力－歪み曲線のグラフであって、横軸にひずみを取り、縦軸に応力を取ったグラフである。
　図１において、ニオブ（Ｎｂ）、鉄（Ｆｅ）の含有量を固定して、アルミニウム（Ａｌ）の含有量（濃度）を変化させた場合に、どのような特性の変化が起こるか確認をした。具体的には、合金３～１０、１７～１９について、ヤング率と最大応力をグラフ状にプロットした。したがって、図１Ａに示すように、さらに、アルミニウムが２ａｔ％未満の場合、合金１７，１８に示すように、ヤング率が高くなりすぎる問題がある。一方で、アルミニウムが、１４ａｔ％以上になると、合金１９（および合金２０）に示すように、ヤング率が再び高くなり且つ加工性も悪化する問題がある。
　図２に示すように、応力－歪み曲線の立ち上がりの角度が、ヤング率に相当するが、合金１７，１９は、角度が高い（＝ヤング率が高い）が、合金５では、角度が低く（ヤング率が低く）なっている。 FIG. 1 shows the results of evaluating changes in the properties of the alloy when the concentration of aluminum is changed. FIG. 1A is a graph in which the horizontal axis indicates the aluminum content and the vertical axis indicates the Young's modulus. FIG. It is the graph which took the content of aluminum on the axis | shaft, and took the maximum stress on the vertical axis | shaft.
FIG. 2 is an explanatory diagram comparing the concentration dependence of aluminum, and is a graph of stress-strain curves of alloys 5, 17 and 19, with the horizontal axis representing strain and the vertical axis representing stress. .
In FIG. 1, when the content of niobium (Nb) and iron (Fe) was fixed and the content (concentration) of aluminum (Al) was changed, it was confirmed what kind of characteristic change occurred. . Specifically, for alloys 3 to 10 and 17 to 19, Young's modulus and maximum stress were plotted in a graph. Therefore, as shown in FIG. 1A, when the aluminum content is less than 2 at%, there is a problem that the Young's modulus becomes too high as shown in alloys 17 and 18. On the other hand, when the aluminum content is 14 at% or more, as shown in the alloy 19 (and the alloy 20), there is a problem that the Young's modulus increases again and the workability deteriorates.
As shown in FIG. 2, the rising angle of the stress-strain curve corresponds to the Young's modulus, but the alloys 17 and 19 have a high angle (= high Young's modulus), but the alloy 5 has a low angle ( Young's modulus is low).
　図３は鉄の濃度を変化させた場合の合金の特性の変化を評価した結果であり、図３Ａは横軸に鉄の含有量を取り縦軸にヤング率を取ったグラフ、図３Ｂは横軸に鉄の含有量を取り縦軸に最大応力を取ったグラフである。
　図４は鉄の濃度依存性を対比する説明図であり、合金５，１５，２３の応力－歪み曲線のグラフであって、横軸にひずみを取り、縦軸に応力を取ったグラフである。
　図３において、ニオブ（Ｎｂ）、アルミニウム（Ａｌ）の含有量を固定して、鉄（Ｆｅ）の含有量（濃度）を変化させた場合に、どのような特性の変化が起こるか確認をした。具体的には、合金２，５，１１，１２，１５，１６，２１～２３について、ヤング率と最大応力をグラフ状にプロットした。したがって、図３、図４からわかるように、鉄が２ａｔ％未満の場合、合金１５，１６に示すように、最大応力（強度）が低くなる問題がある。一方で、鉄が６ａｔ％以上の場合には、合金２１～２３に示すように、ヤング率が高くなりすぎる問題がある。 FIG. 3 is a result of evaluating the change in the characteristics of the alloy when the iron concentration is changed. FIG. 3A is a graph in which the horizontal axis indicates the iron content and the vertical axis indicates the Young's modulus. FIG. It is the graph which took iron content on the axis | shaft, and took the maximum stress on the vertical axis | shaft.
FIG. 4 is an explanatory diagram comparing the concentration dependence of iron, and is a graph of stress-strain curves of alloys 5, 15, and 23, with the horizontal axis representing strain and the vertical axis representing stress. .
In FIG. 3, when the content (concentration) of iron (Fe) was changed while the contents of niobium (Nb) and aluminum (Al) were fixed, it was confirmed what kind of characteristic change occurred. . Specifically, for the alloys 2, 5, 11, 12, 15, 16, 21 to 23, Young's modulus and maximum stress were plotted in a graph. Therefore, as can be seen from FIGS. 3 and 4, when iron is less than 2 at%, as shown in alloys 15 and 16, there is a problem that the maximum stress (strength) is lowered. On the other hand, when iron is 6 at% or more, there is a problem that the Young's modulus becomes too high as shown in alloys 21 to 23.
　図５は既存の合金と実施例の合金との対比説明図であり、横軸にヤング率を取り縦軸に引っ張り強さを取ったグラフである。
　よって、実施例の合金では、１ａｔ％以上５ａｔ％以下のニオブと、２ａｔ％以上５ａｔ％以下の鉄と、２ａｔ％以上１２ａｔ％以下のアルミニウムと、を含有するチタン合金により、特許文献１～１０に示す合金に比べて、ヤング率が５０［ＧＰａ］未満、且つ、強度が６００［ＭＰａ］以上であると共に、加工性がよい合金を提供することができる。
　図５に示すように、一般の鉄系の合金やチタン合金、アルミ合金、マグネシウム合金では、ヤング率が高くなると強度が高くなり、ヤング率が低くなると強度が低くなる傾向がある。これらに対して、合金５に示すように実施例の合金では、５０［ＧＰａ］未満の低ヤング率を実現しつつ、高強度のチタン合金を実現できる。したがって、低ヤング率、高強度で、加工性もよく、生体適合性の高いチタン合金を提供することができる。 FIG. 5 is an explanatory diagram for comparison between the existing alloy and the alloy of the example, and is a graph in which Young's modulus is taken on the horizontal axis and tensile strength is taken on the vertical axis.
Therefore, in the alloys of Examples, Patent Documents 1 to 10 are made of titanium alloys containing 1 at% or more and 5 at% or less of niobium, 2 at% or more and 5 at% or less of iron, and 2 at% or more and 12 at% or less of aluminum. Compared with the alloy shown in FIG. 1, an alloy having a Young's modulus of less than 50 [GPa] and a strength of 600 [MPa] or more and good workability can be provided.
As shown in FIG. 5, in a general iron-based alloy, titanium alloy, aluminum alloy, and magnesium alloy, the strength increases as the Young's modulus increases, and the strength tends to decrease as the Young's modulus decreases. On the other hand, as shown in alloy 5, the alloy of the example can realize a high strength titanium alloy while realizing a low Young's modulus of less than 50 [GPa]. Therefore, a titanium alloy having a low Young's modulus, high strength, good workability, and high biocompatibility can be provided.
　また、実施例の合金では、Ｎｂが１５ａｔ％以下であると共に、ＦｅとＡｌという比較的価格の安い元素を使用しているため、ＶやＺｒ、Ｍｏ、Ｗのような、いわゆるレアメタルを使用する従来の合金に比べて、製造コストも低減することができる。
　また、一般に、チタン合金では、Ｔｉ－Ｎｉ合金以外のチタン系の合金は、融点が高く、溶かして製造、加工等をするために、大がかりな施設が必要になる問題がある。これに対して、実施例の合金では、ＦｅやＡｌが添加されているため、合金の融点が下がりやすい。したがって、高温にしなくても製造等が可能であり、製造コストも低減することが期待できる。 Further, in the alloys of the examples, Nb is 15 at% or less, and since relatively inexpensive elements such as Fe and Al are used, so-called rare metals such as V, Zr, Mo, and W are used. Compared to conventional alloys, the manufacturing cost can also be reduced.
In general, titanium alloys other than Ti—Ni alloys have a high melting point, and there is a problem that a large-scale facility is required for melting, manufacturing and processing. On the other hand, in the alloy of the example, since Fe and Al are added, the melting point of the alloy tends to be lowered. Therefore, it is possible to manufacture without increasing the temperature, and it can be expected to reduce the manufacturing cost.
　以上、本発明の実施例を詳述したが、本発明は、前記実施例に限定されるものではなく、特許請求の範囲に記載された本発明の要旨の範囲内で、種々の変更を行うことが可能である。
　例えば、高い生体適合性を利用して、人工骨やインプラント、歯列矯正ワイヤ等の手術や治療等で使用される生体・医療部材に好適に利用可能であるが、これに限定されない。例えば、低ヤング率（高柔軟性）、高強度を利用して、眼鏡のフレームやゴルフクラブ、サスペンションやスプリング等の自動車、二輪車用部品、テントのポール等のレジャー用品等にも好適に適用可能である。 As mentioned above, although the Example of this invention was explained in full detail, this invention is not limited to the said Example, A various change is performed within the range of the summary of this invention described in the claim. It is possible.
For example, using high biocompatibility, it can be suitably used for a living body / medical member used in an operation or treatment such as an artificial bone, an implant, or an orthodontic wire, but is not limited thereto. For example, using low Young's modulus (high flexibility) and high strength, it can be suitably applied to glasses frames, golf clubs, automobiles such as suspensions and springs, motorcycle parts, and leisure goods such as tent poles. It is.

Claims (2)

  1. 　１ａｔ％以上１５ａｔ％以下のニオブと、
    　２ａｔ％以上５ａｔ％以下の鉄と、
    　２ａｔ％以上１２ａｔ％以下のアルミニウムと、
    　残部のチタンと、
    　不可避的不純物と、
    　からなることを特徴とするチタン合金。     1 to 15 at% niobium,
    2at% or more and 5at% or less of iron,
    Aluminum of 2 at% or more and 12 at% or less,
    The remaining titanium,
    With inevitable impurities,
    A titanium alloy characterized by comprising:
  2. 　請求項１に記載のチタン合金により構成されたことを特徴とする人工骨。 An artificial bone comprising the titanium alloy according to claim 1.
PCT/JP2014/077190 2013-11-01 2014-10-10 Titanium alloy and artificial bone WO2015064343A1 (en)

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH07278704A (en) * 1994-04-14 1995-10-24 Nippon Steel Corp High strength titanium alloy
JP2008006445A (en) * 2006-06-27 2008-01-17 Tohoku Univ Method for joining titanium alloy and aluminum material
JP2008196044A (en) * 2006-04-04 2008-08-28 Daido Steel Co Ltd Beta-type titanium alloy and product thereof
JP2012052219A (en) * 2010-08-03 2012-03-15 Kobe Steel Ltd α-β TITANIUM ALLOY EXTRUDED MATERIAL EXCELLENT IN FATIGUE STRENGTH, AND METHOD FOR PRODUCING THE α-β TITANIUM ALLOY EXTRUDED MATERIAL

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH07278704A (en) * 1994-04-14 1995-10-24 Nippon Steel Corp High strength titanium alloy
JP2008196044A (en) * 2006-04-04 2008-08-28 Daido Steel Co Ltd Beta-type titanium alloy and product thereof
JP2008006445A (en) * 2006-06-27 2008-01-17 Tohoku Univ Method for joining titanium alloy and aluminum material
JP2012052219A (en) * 2010-08-03 2012-03-15 Kobe Steel Ltd α-β TITANIUM ALLOY EXTRUDED MATERIAL EXCELLENT IN FATIGUE STRENGTH, AND METHOD FOR PRODUCING THE α-β TITANIUM ALLOY EXTRUDED MATERIAL

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