JP5083965B2 - Casting compressor impeller - Google Patents
Casting compressor impeller Download PDFInfo
- Publication number
- JP5083965B2 JP5083965B2 JP2007338689A JP2007338689A JP5083965B2 JP 5083965 B2 JP5083965 B2 JP 5083965B2 JP 2007338689 A JP2007338689 A JP 2007338689A JP 2007338689 A JP2007338689 A JP 2007338689A JP 5083965 B2 JP5083965 B2 JP 5083965B2
- Authority
- JP
- Japan
- Prior art keywords
- compressor impeller
- cast
- impeller
- elongation
- hub
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Fee Related
Links
- 238000005266 casting Methods 0.000 title description 18
- 229910052804 chromium Inorganic materials 0.000 claims description 6
- 229910052745 lead Inorganic materials 0.000 claims description 6
- 229910052718 tin Inorganic materials 0.000 claims description 6
- 229910052725 zinc Inorganic materials 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 5
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- 239000011159 matrix material Substances 0.000 description 12
- 229910052802 copper Inorganic materials 0.000 description 11
- 229910045601 alloy Inorganic materials 0.000 description 9
- 239000000956 alloy Substances 0.000 description 9
- 229910052759 nickel Inorganic materials 0.000 description 9
- 230000000694 effects Effects 0.000 description 8
- 229910052749 magnesium Inorganic materials 0.000 description 7
- 230000035882 stress Effects 0.000 description 7
- 229910000765 intermetallic Inorganic materials 0.000 description 6
- 239000006104 solid solution Substances 0.000 description 6
- 238000002485 combustion reaction Methods 0.000 description 5
- 239000013078 crystal Substances 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 238000001556 precipitation Methods 0.000 description 5
- 229910019018 Mg 2 Si Inorganic materials 0.000 description 4
- 229910018505 Ni—Mg Inorganic materials 0.000 description 4
- 239000000654 additive Substances 0.000 description 4
- 230000000996 additive effect Effects 0.000 description 4
- 230000032683 aging Effects 0.000 description 4
- 230000007547 defect Effects 0.000 description 4
- 239000000243 solution Substances 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 4
- 229910000979 O alloy Inorganic materials 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 238000000034 method Methods 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 229910000861 Mg alloy Inorganic materials 0.000 description 2
- 229910010038 TiAl Inorganic materials 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 238000002425 crystallisation Methods 0.000 description 2
- 230000008025 crystallization Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- 229910018565 CuAl Inorganic materials 0.000 description 1
- 229910003322 NiCu Inorganic materials 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000000151 deposition Methods 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 229910052602 gypsum Inorganic materials 0.000 description 1
- 239000010440 gypsum Substances 0.000 description 1
- 238000001513 hot isostatic pressing Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000010111 plaster casting Methods 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
Images
Landscapes
- Structures Of Non-Positive Displacement Pumps (AREA)
Description
本発明は、例えば過給機に使用されるコンプレッサ羽根車などに好適な高強度を有する鋳造コンプレッサ羽根車に関する。 The present invention relates to a cast compressor impeller having high strength suitable for, for example, a compressor impeller used for a supercharger.
例えば、自動車や船舶等の内燃機関に組み込まれる過給機に使用されるコンプレッサ羽根車は、高温に曝されることのない外気を吸気する部分で利用される。また、コスト的な有利性を考慮し、通常は、例えば、米国材料試験協会（ＡＳＴＭ）規定の３５４．０合金（Ａｌ−９％Ｓｉ−１．８％Ｃｕ−０．５％Ｍｇ合金）や３５５．０合金（Ａｌ−５％Ｓｉ−１．３％Ｃｕ−０．５％Ｍｇ合金）などのアルミニウム鋳造合金製の鋳造コンプレッサ羽根車が多く使用されている。 For example, a compressor impeller used in a supercharger incorporated in an internal combustion engine such as an automobile or a ship is used in a portion that sucks outside air that is not exposed to high temperatures. In consideration of cost advantages, for example, 354.0 alloy (Al-9% Si-1.8% Cu-0.5% Mg alloy) defined by the American Society for Testing and Materials (ASTM) Cast compressor impellers made of cast aluminum alloys such as 355.0 alloy (Al-5% Si-1.3% Cu-0.5% Mg alloy) are often used.
近年、内燃機関の燃焼効率をさらに向上させる目的で、過給機をより高速回転させるための種々の検討がなされている。これらの検討によれば、高速回転により、コンプレッサ羽根車に作用する遠心力は増大し、現状は１５０℃程度の曝露温度が１８０℃にまで上昇すると予測されている。このため、鋳造コンプレッサ羽根車には、常温においては、破断伸びで５％以上とされる適度な靭性と、更なる高強度が必要となる。 In recent years, in order to further improve the combustion efficiency of an internal combustion engine, various studies for rotating a supercharger at higher speed have been made. According to these studies, the centrifugal force acting on the compressor impeller is increased by high-speed rotation, and it is predicted that the exposure temperature of about 150 ° C. will rise to 180 ° C. at present. For this reason, the cast compressor impeller requires moderate toughness that is 5% or more at break elongation at room temperature and further high strength.
例えば、高強度の鋳造コンプレッサ羽根車としては、特許文献１の実施例において、引張強さや破断伸びは不明であるが、０．２％耐力については、室温で４２１ＭＰａ、温度１８０℃で２９８ＭＰａを有する鋳造コンプレッサ羽根車が提案されている。この鋳造コンプレッサ羽根車は、質量％で、Ｃｕ：３．２％、Ｎｉ：０．８９％、Ｍｇ：１．２２％、Ｔｉ：０．３１％、Ｓｉ：０．１９％、Ｆｅ：１．８０％を含み、残部ＡｌでなるＡｌ−Ｃｕ−Ｎｉ−Ｍｇ系合金が使用されている。 For example, as a high-strength cast compressor impeller, in the example of Patent Document 1, the tensile strength and elongation at break are unknown, but the 0.2% proof stress has 421 MPa at room temperature and 298 MPa at 180 ° C. A cast compressor impeller has been proposed. This cast compressor impeller is, by mass%, Cu: 3.2%, Ni: 0.89%, Mg: 1.22%, Ti: 0.31%, Si: 0.19%, Fe: 1. An Al—Cu—Ni—Mg alloy containing 80% and the balance being Al is used.
上述した特許文献１に提案される鋳造コンプレッサ羽根車は、０．２％耐力が室温で４２１ＭＰａと高く、これに加えて温度１８０℃でも２９８ＭＰａと高く、確かに従来の３５４．０合金などよりも耐熱性が優れている。しかしながら、特許文献１が開示しない破断伸びに関わる不具合が懸念された。具体的には、金属間化合物の析出などにより合金の脆化を引き起こしやすいＣｕ、Ｎｉ、Ｆｅを多く含み、特にＣｕやＮｉよりも脆化への影響が大きいとされるＦｅを多量に含むことから、上述したように鋳造コンプレッサ羽根車に必要とされる常温での５％以上の破断伸びが得られないことが懸念された。 The cast compressor impeller proposed in Patent Document 1 described above has a 0.2% proof stress as high as 421 MPa at room temperature, and in addition to this, it is as high as 298 MPa even at a temperature of 180 ° C. It is certainly higher than the conventional 354.0 alloy and the like. Excellent heat resistance. However, there has been a concern about defects related to elongation at break which is not disclosed in Patent Document 1. Specifically, it contains a large amount of Cu, Ni, and Fe that are likely to cause embrittlement of the alloy due to precipitation of intermetallic compounds, etc., and especially contains a large amount of Fe that is considered to have a greater effect on embrittlement than Cu and Ni. Thus, as described above, there was a concern that the elongation at break of 5% or more at room temperature required for the cast compressor impeller could not be obtained.
本発明の目的は、常温において、破断伸びで５％以上とされる適度な靭性と、更なる高強度を得ることができる、鋳造コンプレッサ羽根車を提供することである。 An object of the present invention is to provide a cast compressor impeller capable of obtaining an appropriate toughness of 5% or more at break elongation and a further high strength at room temperature.
本発明者は、前記課題に鑑み、従来のＡｌ−Ｃｕ−Ｎｉ−Ｍｇ系合金において、常温において破断伸びで５％以上とされる適度な靭性と更なる高強度を有し、望ましくは１８０℃といった高温においても良好な強度を持たせることを検討した。そして、脆化に関わるＣｕとＮｉの含有量の配分を勘案し、Ａｌに対するＣｕ、Ｎｉ、Ｍｇの含有量を最適化することにより、前記課題を解決できることを見出し本発明に到達した。 In view of the above problems, the inventor of the present invention has a moderate toughness and a further high strength that are 5% or more at break elongation at room temperature in a conventional Al—Cu—Ni—Mg alloy, preferably 180 ° C. We examined to give good strength even at such high temperatures. Then, in consideration of the distribution of Cu and Ni contents related to embrittlement, the inventors have found that the above problems can be solved by optimizing the contents of Cu, Ni, and Mg with respect to Al.
すなわち、本発明の鋳造コンプレッサ羽根車は、ハブ軸部と、該ハブ軸部から半径方向に延在するとともにハブ面とディスク面を有するハブディスク部と、前記ハブ面に配設された複数の羽根部とを有してなる鋳造コンプレッサ羽根車であって、該鋳造コンプレッサ羽根車は、質量％で、４．５％＜Ｃｕ≦５．７％、０．８％≦Ｎｉ≦２．５％、１．２％≦Ｍｇ≦２．５％、０．０５％≦Ｔｉ≦０．２％、０．２％≦Ｓｉ≦１．０％、０．０５％≦Ｆｅ≦０．２％、Ｂ≦０．０６％、残部Ａｌおよび不可避的不純物からなる組成を有し、該不可避的不純物のうちＭｎ、Ｚｎ、Ｐｂ、Ｓｎ、Ｃｒはそれぞれ質量％でＭｎ≦０．１％、Ｚｎ≦０．１％、Ｐｂ≦０．１％、Ｓｎ≦０．１％、Ｃｒ≦０．１％に規制されており、かつ、常温（２５℃）における破断伸びが５％以上、０．２％耐力が３６０ＭＰａ以上を有する、鋳造コンプレッサ羽根車である。 That is, the cast compressor impeller of the present invention includes a hub shaft portion, a hub disk portion extending in a radial direction from the hub shaft portion and having a hub surface and a disk surface, and a plurality of hub disks disposed on the hub surface. A cast compressor impeller having blade portions, the cast compressor impeller being 4.5% <Cu ≦ 5.7%, 0.8% ≦ Ni ≦ 2.5% by mass%. 1.2% ≦ Mg ≦ 2.5%, 0.05% ≦ Ti ≦ 0.2%, 0.2% ≦ Si ≦ 1.0%, 0.05% ≦ Fe ≦ 0.2%, B ≦ 0.06%, and the composition is composed of the balance Al and unavoidable impurities. Among these unavoidable impurities, Mn, Zn, Pb, Sn, and Cr are Mn ≦ 0.1% and Zn ≦ 0. 1%, Pb ≦ 0.1%, Sn ≦ 0.1%, Cr ≦ 0.1%, and normal temperature (25 ° C.) Elongation at break of definitive more than 5%, 0.2% proof stress has more than 360 MPa, a cast compressor impeller.
また、本発明の鋳造コンプレッサ羽根車は、複数の羽根部が交互に配列された長羽根と短羽根からなる、鋳造コンプレッサ羽根車であっても良い。 The cast compressor impeller of the present invention may be a cast compressor impeller composed of long blades and short blades in which a plurality of blade portions are alternately arranged.
本発明の鋳造コンプレッサ羽根車は、従来の鋳造コンプレッサ羽根車に比べ、常温（２５℃）において破断伸びで５％以上とされる適度な伸びを有しつつ３６０ＭＰａ以上の０．２％耐力を有することができる。よって、例えば自動車などに搭載される過給機用のコンプレッサ羽根車に適用することにより、従来よりも高速回転でも使用可能となることが期待できるので、本発明は工業上極めて有益な技術となる。 The cast compressor impeller of the present invention has a 0.2% proof stress of 360 MPa or more while having a moderate elongation of 5% or more at room temperature (25 ° C.) in breaking elongation as compared with a conventional cast compressor impeller. be able to. Therefore, for example, by applying to a compressor impeller for a supercharger mounted on an automobile or the like, it can be expected that it can be used even at a higher rotational speed than before, so the present invention is an extremely useful technology in the industry. .
本発明の鋳造コンプレッサ羽根車における重要な特徴は、従来のＡｌ−Ｃｕ−Ｎｉ−Ｍｇ系合金において、上述した特許文献１のように脆化への影響が大きいとされるＦｅを添加するのではなく、Ｃｕをさらに添加し、ＮｉとＣｕの含有量、およびＭｇの含有量を最適化したことである。
以下、本発明の鋳造コンプレッサ羽根車における、Ａｌに対する添加元素と各添加元素の含有量の限定理由について詳細に説明する。また、各合金元素の含有量は、特に断らない場合には質量％で示す。
An important feature of the cast compressor impeller of the present invention is that, in the conventional Al—Cu—Ni—Mg alloy, Fe that is considered to have a great influence on embrittlement as described in Patent Document 1 is added. However, Cu was further added to optimize the contents of Ni and Cu and the contents of Mg.
Hereinafter, the reasons for limiting the additive elements with respect to Al and the contents of each additive element in the cast compressor impeller of the present invention will be described in detail. Further, the content of each alloy element is indicated by mass% unless otherwise specified.
本発明においては、常温での高強度化のために、まずＣｕおよびＭｇの含有量を最適化した。ＣｕおよびＭｇは、Ａｌマトリックス内に固溶することで強度を向上させる固溶強化や、鋳造後に熱処理（例えばＴ６処理：ＪＩＳ−Ｈ０００１）を施すことで強度を向上させる析出強化といった作用効果を有する重要な元素である。 In the present invention, the contents of Cu and Mg were first optimized in order to increase the strength at room temperature. Cu and Mg have effects such as solid solution strengthening that improves the strength by dissolving in the Al matrix and precipitation strengthening that improves the strength by performing heat treatment after casting (for example, T6 treatment: JIS-H0001). It is an important element.
４．５％＜Ｃｕ≦５．７％
本発明において、Ｃｕ含有量は４．５％を超え５．７％以下とし、これにより脆化による破断伸び低下を引き起こすことなく十分な強度を得る。Ｃｕは、上述したように固溶と析出により強度を向上させる効果を有する。しかし、Ｃｕが４．５％以下では固溶と析出の両方を同時に得られず強度向上が不十分になることがある。また、Ｃｕが５．７％を超えると粒界にＣｕＡｌ２（θ相）等の金属間化合物が多量に晶出したり析出したりするので破断伸びを低下させることがある。
4.5% <Cu ≦ 5.7%
In the present invention, the Cu content is more than 4.5% and not more than 5.7%, thereby obtaining sufficient strength without causing a decrease in elongation at break due to embrittlement. Cu has the effect of improving strength by solid solution and precipitation as described above. However, if Cu is 4.5% or less, both solid solution and precipitation cannot be obtained simultaneously, and strength improvement may be insufficient. On the other hand, if Cu exceeds 5.7%, a large amount of intermetallic compounds such as CuAl 2 (θ phase) may be crystallized or precipitated at the grain boundaries, which may reduce the elongation at break.
１．２％≦Ｍｇ≦２．５％
本発明において、Ｍｇ含有量は１．２％以上２．５％以下とし、これによりＡｌマトリックス内にＭｇを固溶させる。もしくは、ＭｇとＳｉとで金属間化合物（Ｍｇ２Ｓｉ）を生成させて固溶させる。これにより、破断伸びを向上させる作用効果を得る。よって、Ｍｇ含有量を好適にすることで、適度な破断伸びを有する鋳造合金となることが期待できる。しかし、Ｍｇが１．２％未満では固溶量が少なすぎて固溶強化が期待できない。また、Ｍｇが２．５％を超えると破断伸びを低下させてしまうことがある。好ましくは、１．５％以上、２．０％以下である。
1.2% ≦ Mg ≦ 2.5%
In the present invention, the Mg content is 1.2% or more and 2.5% or less, so that Mg is dissolved in the Al matrix. Alternatively, an intermetallic compound (Mg 2 Si) is generated and dissolved in Mg and Si. Thereby, the effect which improves breaking elongation is acquired. Therefore, by making the Mg content suitable, it can be expected to be a cast alloy having an appropriate breaking elongation. However, if Mg is less than 1.2%, the amount of solid solution is too small and solid solution strengthening cannot be expected. If Mg exceeds 2.5%, the elongation at break may be reduced. Preferably, it is 1.5% or more and 2.0% or less.
０．８％≦Ｎｉ≦２．５％
本発明において、Ｎｉ含有量は上述のＣｕおよびＭｇの含有量を考慮し、０．８％以上２．５％以下とする。適量のＮｉを含ませると、Ｎｉ系の金属間化合物が生成され、これにより特に高温での強度を向上させることができ、１８０℃といった将来予想される高温下での使用に有効である。しかし、Ｎｉが０．８％未満ではＮｉ系の金属間化合物の晶出量あるいは析出量が不足するので強度の向上が期待できない。また、Ｎｉが２．５％を超えると、Ｎｉ系の晶出物あるいは析出物が過剰に生成されてしまい破断伸びを低下させることがある。また、ＮｉはＣｕとで粒界にＡｌ５ＮｉＣｕ（Ｙ相）を生成させやすいので、Ａｌマトリックス内のＣｕの固溶量が不十分となって強度の低下をもたらすことがある。好ましくは、１．０％以上、２．０％以下である。
0.8% ≦ Ni ≦ 2.5%
In the present invention, the Ni content is set to 0.8% or more and 2.5% or less in consideration of the contents of Cu and Mg described above. When an appropriate amount of Ni is included, a Ni-based intermetallic compound is generated, whereby the strength at a particularly high temperature can be improved, and it is effective for use at a predicted high temperature such as 180 ° C. in the future. However, if Ni is less than 0.8%, the crystallization amount or precipitation amount of the Ni-based intermetallic compound is insufficient, so that improvement in strength cannot be expected. On the other hand, if Ni exceeds 2.5%, Ni-based crystallized substances or precipitates are excessively generated, and the elongation at break may be lowered. Further, since Ni easily forms Al 5 NiCu (Y phase) at the grain boundary with Cu, the amount of Cu in the Al matrix is insufficient, which may lead to a decrease in strength. Preferably, it is 1.0% or more and 2.0% or less.
０．０５％≦Ｔｉ≦０．２％
本発明において、Ｔｉを０．０５％以上０．２％以下で含むと、Ａｌマトリックスが生成される過程で、ＴｉＡｌ３等の結晶核が結晶粒界に晶出する。これにより、Ａｌマトリックスの結晶粒の成長を抑制し、Ａｌマトリックスの結晶粒を微細化させる。Ａｌマトリックス自体の結晶粒を微細化することにより、強度のさらなる改善が期待できる。しかし、Ｔｉが０．２％を超えるとＴｉＡｌ３等の晶出が過剰となって破断伸びを低下させることがある。好ましくは、０．０５％以上、０．１５％以下である。
0.05% ≦ Ti ≦ 0.2%
In the present invention, when Ti is contained at 0.05% or more and 0.2% or less, crystal nuclei such as TiAl 3 are crystallized at the grain boundaries in the process of forming the Al matrix. Thereby, the growth of crystal grains of the Al matrix is suppressed, and the crystal grains of the Al matrix are refined. Further improvement in strength can be expected by refining the crystal grains of the Al matrix itself. However, if Ti exceeds 0.2%, crystallization of TiAl 3 or the like may be excessive and the elongation at break may be reduced. Preferably, it is 0.05% or more and 0.15% or less.
０．２％≦Ｓｉ≦１．０％
本発明においては、Ｍｇ含有量を考慮し、Ｓｉ含有量を１．０％以下とする。ＳｉはＭｇと結び付いてＭｇ２Ｓｉを生成する。このＭｇ２Ｓｉを溶体化処理によりＡｌマトリックス内へ固溶させ、次いで時効処理により均一かつ微細に析出させることにより、常温での強度がさらに向上することが期待できる。しかし、Ｓｉが１．０％を超えるとＡｌマトリックス内に固溶しきれないＳｉが析出物として粒界に残存し、これにより破断伸びを劣化させることがある。また、Ｓｉは、Ｍｇに対して優先的に結合するため、Ａｌマトリックス内に固溶するＭｇ量が減少することとなり、破断伸びや強度を低下させることがある。こうなると、適度な伸びと強度が望まれる鋳造コンプレッサ羽根車の用途には致命的である。一方、Ｓｉが０．２％未満では、Ｍｇとで生成される金属間化合物（Ｍｇ２Ｓｉ）による固溶強化が得られず、破断伸びをさらに向上させる作用効果が得られない。
0.2% ≦ Si ≦ 1.0%
In the present invention, considering the Mg content, the Si content is 1.0% or less. Si combines with Mg to produce Mg 2 Si. It is expected that the strength at normal temperature is further improved by solid-dissolving this Mg 2 Si into the Al matrix by solution treatment and then depositing it uniformly and finely by aging treatment. However, when Si exceeds 1.0%, Si that cannot be completely dissolved in the Al matrix remains as a precipitate at the grain boundary, which may deteriorate the elongation at break. Further, since Si is preferentially bonded to Mg, the amount of Mg dissolved in the Al matrix is reduced, which may reduce the elongation at break and strength. This is fatal for cast compressor impeller applications where moderate elongation and strength are desired. On the other hand, if Si is less than 0.2%, solid solution strengthening by the intermetallic compound (Mg 2 Si) produced with Mg cannot be obtained, and the effect of further improving the elongation at break cannot be obtained.
０．０５％≦Ｆｅ≦０．２％
Ｆｅは、過剰に含むと脆化を引き起こしやすい元素であるが、適量に含むと強度の向上が期待できる。また、Ｆｅは鋳造過程において混入しやすい元素でもある。よって、本発明においては、ＣｕとＮｉの含有量を考慮し、Ｆｅを０．０５％以上０．２％以下で含有させる。好ましくは、０．１％以上、０．２％以下である。
0.05% ≦ Fe ≦ 0.2%
Fe is an element that tends to cause embrittlement if included excessively, but if it is included in an appropriate amount, improvement in strength can be expected. Fe is also an element easily mixed in the casting process. Therefore, in the present invention, considering the contents of Cu and Ni, Fe is contained in an amount of 0.05% to 0.2%. Preferably, it is 0.1% or more and 0.2% or less.
Ｂ≦０．０６％
本発明においては、Ｔｉの原料として純Ｔｉを使用するよりもＴｉＢを使用することでコスト面で格段に有利となる。この場合には、Ｔｉ含有量の２０％程度のＢを含むように調整することが望ましい。これにより、ＢはＴｉＢ２等を生成し、Ａｌマトリックスの結晶粒の微細化を促進させるといった、Ｔｉの作用効果をより高めるように作用する。例えば、Ｔｉ含有量が０．０５％〜０．２％である場合、Ｂは０．００１％〜０．０６％となるように調整することが望ましい。この場合、０．０６％を超えてＢを含ませても効果の向上は期待できず、ＴｉＢ２等が多量に晶出することとなって伸びを低下させることがある。
B ≦ 0.06%
In the present invention, using TiB rather than using pure Ti as a raw material for Ti is extremely advantageous in terms of cost. In this case, it is desirable to adjust so as to contain B of about 20% of the Ti content. Thereby, B acts to enhance Ti's action and effect such as generating TiB 2 or the like and promoting the refinement of crystal grains of the Al matrix. For example, when the Ti content is 0.05% to 0.2%, it is desirable to adjust B to be 0.001% to 0.06%. In this case, even if it contains B exceeding 0.06%, the improvement of the effect cannot be expected, and TiB 2 or the like may crystallize in a large amount, thereby reducing the elongation.
上述したいずれの元素も、Ａｌに対して適量を含むことによって有効な作用効果が得られる元素である。これらの元素以外の残部は、構造用合金として軽量であって比強度に優れるマトリックスとなるＡｌと、不可避的不純物である。特に溶解などの製造過程で含まれやすい元素としてＭｎ、Ｚｎ、Ｐｂ、Ｓｎ、Ｃｒがある。これらの不純物元素は、多量に含むと上述した添加元素の作用を阻害するため、Ｍｎ≦０．１％、Ｚｎ≦０．１％、Ｐｂ≦０．１％、Ｓｎ≦０．１％、Ｃｒ≦０．１％に規制することが必要である。 Any of the above-described elements is an element that can obtain an effective action and effect by including an appropriate amount with respect to Al. The balance other than these elements is Al, which is a lightweight matrix as a structural alloy, and has an excellent specific strength, and unavoidable impurities. In particular, there are Mn, Zn, Pb, Sn, and Cr as elements that are likely to be included in the manufacturing process such as dissolution. When these impurity elements are contained in a large amount, the action of the above-described additive elements is hindered, so Mn ≦ 0.1%, Zn ≦ 0.1%, Pb ≦ 0.1%, Sn ≦ 0.1%, Cr It is necessary to regulate to ≦ 0.1%.
本発明の鋳造コンプレッサ羽根車は、上述した組成の溶湯を鋳造して得ることができる。そして、得られた鋳造羽根車に対し、溶体化処理の後に時効処理を各々の処理条件を調整し、熱処理として、例えばＴ６処理（ＪＩＳ−Ｈ０００１）を施すことにより、常温（２５℃）において、破断伸びが５％以上、０．２％耐力が３６０ＭＰａ以上を有する鋳造コンプレッサ羽根車を得ることができる。なお、鋳造コンプレッサ羽根車の製造過程において、前記熱処理を施す前にＨＩＰ処理（熱間静水圧加圧処理）を施すこともできる。 The cast compressor impeller of the present invention can be obtained by casting the molten metal having the composition described above. And with respect to the obtained cast impeller, by adjusting each treatment condition of the aging treatment after the solution treatment, by performing, for example, T6 treatment (JIS-H0001), at normal temperature (25 ° C.), A cast compressor impeller having a breaking elongation of 5% or more and a 0.2% proof stress of 360 MPa or more can be obtained. In the manufacturing process of the cast compressor impeller, HIP processing (hot isostatic pressing) can be performed before the heat treatment.
このように、常温（２５℃）において、破断伸びが５％以上、０．２％耐力が３６０ＭＰａ以上を有する本発明の鋳造コンプレッサ羽根車は、従来のＡｌ−Ｃｕ−Ｎｉ−Ｍｇ系合金では強度が不十分で適用できなかった高速回転領域での使用に耐えることができる鋳造コンプレッサ羽根車となる。 Thus, at room temperature (25 ° C.), the cast compressor impeller of the present invention having a breaking elongation of 5% or more and a 0.2% proof stress of 360 MPa or more is a conventional Al—Cu—Ni—Mg alloy. Therefore, it becomes a cast compressor impeller that can withstand use in a high-speed rotation region that was insufficient and could not be applied.
次に、本発明の鋳造コンプレッサ羽根車の形状について説明する。
本発明の鋳造コンプレッサ羽根車は、ハブ軸部と、該ハブ軸部から半径方向に延在するとともにハブ面とディスク面を有するハブディスク部と、前記ハブ面に配設された複数の羽根部とを有してなる。また、複数の羽根部は、長羽根と短羽根とが交互に配列されたものであってよい。
Next, the shape of the cast compressor impeller of the present invention will be described.
A cast compressor impeller according to the present invention includes a hub shaft portion, a hub disk portion extending in a radial direction from the hub shaft portion and having a hub surface and a disk surface, and a plurality of blade portions disposed on the hub surface. It has. Further, the plurality of blade portions may be ones in which long blades and short blades are alternately arranged.
図１、図２に、本発明の鋳造コンプレッサ羽根車の一例を模式的に示す。鋳造コンプレッサ羽根車１（以下、羽根車１という）は、ハブ軸部２と、該ハブ軸部２から半径方向に延在するとともにハブ面４とディスク面５を有するハブディスク部３、前記ハブ面４に配設された複数の羽根部とを含む羽根車形状体である。また、この羽根車１の羽根部は、長羽根６と、短羽根となるスプリッタ羽根７とが交互に配列され、各々が複雑な空力学的曲面形状のブレード面を表裏に有している。このように空力学的に複雑な曲面形状を有することにより、例えば過給機において吸気および圧縮の効率を高めることができ、内燃機関の燃焼効率の向上に寄与できる。
1 and 2 schematically show an example of the cast compressor impeller of the present invention. A cast compressor impeller 1 (hereinafter referred to as an impeller 1) includes a
以下、本発明の鋳造コンプレッサ羽根車につき、実施例によりさらに具体的に説明する。なお、本実施例では、上述した図１、図２に示す羽根車１と同等形状を有する鋳造コンプレッサ羽根車をプラスターモールド鋳造法により製造した。
具体的には、まず、羽根車１に対応する形状を有するゴム模型を製作し、このゴム模型を用いて石膏からなる鋳造用鋳型を製作した。次に、この鋳造用鋳型に、溶解して脱ガス処理したアルミニウム鋳造合金の溶湯を吸上げ式の吸引鋳造法により鋳造した。そして冷却後、鋳造用鋳型を除去し、長羽根６とスプリッタ羽根７およびハブ軸部２が一体に形成された鋳造羽根車を得た。表１における実施例および比較例とも、不回りやヒケ、ピンホールといった鋳造不具合もなく、鋳造羽根車を得ることができた。なお、表１に示す実施例および比較例の化学組成は、最終的に得られた鋳造コンプレッサ羽根車の組成である。
Hereinafter, the cast compressor impeller of the present invention will be described more specifically with reference to examples. In this example, a cast compressor impeller having the same shape as the impeller 1 shown in FIGS. 1 and 2 was manufactured by a plaster mold casting method.
Specifically, first, a rubber model having a shape corresponding to the impeller 1 was manufactured, and a casting mold made of gypsum was manufactured using the rubber model. Next, a molten aluminum casting alloy melted and degassed in this casting mold was cast by a suction type suction casting method. After cooling, the casting mold was removed to obtain a casting impeller in which the
本実施例においては、前記鋳造羽根車に鋳造欠陥が内在していた場合を鑑みて、前記鋳造羽根車に鋳造欠陥があったとしても機械特性を損ねない程度に微小化しておくために、念のため得られた前記鋳造羽根車に対してＨＩＰ処理（熱間静水圧加圧処理）を５２５℃、１０３ＭＰａ、２ｈで実施した。 In this embodiment, in view of the case where a casting defect is inherent in the casting impeller, even if there is a casting defect in the casting impeller, in order to reduce the size so as not to impair mechanical properties, Therefore, HIP treatment (hot isostatic pressure treatment) was performed on the cast impeller obtained at 525 ° C., 103 MPa, and 2 h.
次に、得られた前記鋳造羽根車に対してＴ６処理（溶体化処理および時効処理）を実施した。Ｔ６処理を実施するにあたり、溶体化処理では生産性を考慮し、できる限り保持する時間を短縮できるように選定した。具体的には、ブリスター等を生じ難いと推測される温度であって、できる限り高い温度と考えられる５４０℃を選定し、１２ｈ保持した。これに対し、時効処理では、常温（２５℃）での破断伸びを少なくとも５％以上にすることができると推測される１８０℃を選定し、８ｈ保持した。 Next, T6 treatment (solution treatment and aging treatment) was performed on the obtained cast impeller. In carrying out the T6 treatment, the solution treatment was selected in consideration of productivity, so that the holding time could be shortened as much as possible. Specifically, a temperature of 540 ° C., which is estimated to be as high as possible, was estimated to be difficult to generate blisters, and held for 12 hours. On the other hand, in the aging treatment, 180 ° C., which is estimated to be able to make the elongation at break at room temperature (25 ° C.) at least 5%, was selected and held for 8 hours.
上述した製造方法により、表１に示す化学組成を有する鋳造コンプレッサ羽根車を得ることができた。得られた羽根車１は、例えば自動車のディーゼルエンジン用コンプレッサ羽根車に適用できる形状を有するものであって、最大径φ８０ｍｍ（ハブディスク部３）、全高５５ｍｍ（ハブ軸部２）、長羽根６とスプリッタ羽根７の合計枚数１２枚、羽根先端肉厚０．４〜０．６ｍｍの寸法を有するものである。
A casting compressor impeller having the chemical composition shown in Table 1 could be obtained by the manufacturing method described above. The obtained impeller 1 has a shape applicable to, for example, a compressor impeller for a diesel engine of an automobile, and has a maximum diameter φ80 mm (hub disk portion 3), a total height of 55 mm (hub shaft portion 2), and a
次に、得られた羽根車１のハブディスク３の最大径近傍の厚肉部分から丸棒引張試験片を採取し、常温（２５℃）における破断伸びと０．２％耐力を測定した。測定結果は表１に併記して示す。これらの試験法についてはＪＩＳ−Ｚ２２４１、Ｇ０５６７に記載され、測定した伸びは破断後の標点距離の永久伸びで定義される破断伸びである。
Next, a round bar tensile test piece was sampled from a thick portion near the maximum diameter of the
以上、本発明の鋳造コンプレッサ羽根車は、常温（２５℃）において適度な靭性を有するとされる５．０％以上の破断伸びを有し、３６０ＭＰａ以上の０．２％耐力を有することができた。本実施例により、Ａｌに対するＣｕ、Ｎｉ、Ｍｇなどの添加元素の含有量をより適正化することにより、従来よりも機械特性が良好な鋳造コンプレッサ羽根車が得られることがわかった。 As described above, the cast compressor impeller of the present invention has a breaking elongation of 5.0% or more, which is said to have appropriate toughness at room temperature (25 ° C.), and can have a 0.2% proof stress of 360 MPa or more. It was. According to the present example, it was found that a cast compressor impeller having better mechanical characteristics than the conventional one can be obtained by optimizing the content of additive elements such as Cu, Ni, and Mg with respect to Al.
１．鋳造コンプレッサ羽根車
２．ハブ軸部
３．ハブディスク部
４．ハブ面
５．ディスク面
６．長羽根
７．スプリッタ羽根
1. 1.
Claims (2)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2007338689A JP5083965B2 (en) | 2007-12-28 | 2007-12-28 | Casting compressor impeller |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2007338689A JP5083965B2 (en) | 2007-12-28 | 2007-12-28 | Casting compressor impeller |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2009155715A JP2009155715A (en) | 2009-07-16 |
| JP5083965B2 true JP5083965B2 (en) | 2012-11-28 |
Family
ID=40960026
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2007338689A Expired - Fee Related JP5083965B2 (en) | 2007-12-28 | 2007-12-28 | Casting compressor impeller |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP5083965B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108950314A (en) * | 2018-06-22 | 2018-12-07 | 宁波展欣汽车科技发展有限公司 | The preparation method of fire resistant aluminum alloy automotive hub |
| CN108950313A (en) * | 2018-06-20 | 2018-12-07 | 宁波展欣汽车科技发展有限公司 | The preparation method of high-strength aluminum alloy automotive hub |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107419139A (en) * | 2017-06-27 | 2017-12-01 | 南京律智诚专利技术开发有限公司 | A kind of alloy for airborne vehicle compressor impeller |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH07179977A (en) * | 1993-12-22 | 1995-07-18 | Nippon Steel Corp | High heat resistant aluminum alloy and method for producing the same |
-
2007
- 2007-12-28 JP JP2007338689A patent/JP5083965B2/en not_active Expired - Fee Related
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108950313A (en) * | 2018-06-20 | 2018-12-07 | 宁波展欣汽车科技发展有限公司 | The preparation method of high-strength aluminum alloy automotive hub |
| CN108950314A (en) * | 2018-06-22 | 2018-12-07 | 宁波展欣汽车科技发展有限公司 | The preparation method of fire resistant aluminum alloy automotive hub |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2009155715A (en) | 2009-07-16 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US8292589B2 (en) | Casting aluminum alloy, cast compressor impeller comprising the alloy, and process for producing the same | |
| CN104736271B (en) | Compressor impeller made of Al alloy casting and its manufacturing method | |
| JP5703881B2 (en) | High strength magnesium alloy and method for producing the same | |
| JP5598895B2 (en) | Aluminum die-cast alloy, cast compressor impeller made of this alloy, and method for manufacturing the same | |
| JP4958292B2 (en) | Aluminum die-cast alloy, cast compressor impeller made of this alloy, and method for manufacturing the same | |
| JP6540075B2 (en) | TiAl heat resistant member | |
| JP2007169712A (en) | Aluminum alloy for plastic working | |
| JPH1112674A (en) | Aluminum alloy and aluminum alloy piston for internal combustion engine piston | |
| EP3575423B1 (en) | Preform and method for producing tial-based turbine wheel | |
| JP7358759B2 (en) | Scroll member and scroll forging product manufacturing method | |
| JP5083965B2 (en) | Casting compressor impeller | |
| JPH11246925A (en) | Aluminum alloy casting with high toughness, and its manufacture | |
| JP2008223532A (en) | Manufacturing method for compressor impeller | |
| JP4719583B2 (en) | Unidirectional solidification nickel-base superalloy excellent in strength, corrosion resistance and oxidation resistance and method for producing unidirectional solidification nickel-base superalloy | |
| JP4845201B2 (en) | Aluminum die-cast alloy and compressor impeller using the same | |
| JP2007169731A (en) | Aluminum casting alloy and compressor impeller using the same | |
| JP4905680B2 (en) | Magnesium casting alloy and compressor impeller using the same | |
| JP7131160B2 (en) | Cold forged material for impeller and its manufacturing method | |
| JP7319447B1 (en) | Aluminum alloy material and its manufacturing method | |
| JP2008088460A (en) | High-strength aluminum casting alloy and compressor impeller using the same | |
| JP2008196367A (en) | Cast impeller for compressor and its manufacturing method | |
| JP2020066785A (en) | Extruded material for impeller and method for producing the same | |
| JP2017155268A (en) | Al ALLOY CAST ARTICLE-MADE COMPRESSOR IMPELLER | |
| WO2022211062A1 (en) | Aluminum alloy material, production method therefor, and machine component | |
| JP2019190366A (en) | Forged product for impeller |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20101111 |
|
| A521 | Written amendment |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20111219 |
|
| A977 | Report on retrieval |
Free format text: JAPANESE INTERMEDIATE CODE: A971007 Effective date: 20120824 |
|
| TRDD | Decision of grant or rejection written | ||
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 20120831 |
|
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20120831 |
|
| R150 | Certificate of patent or registration of utility model |
Free format text: JAPANESE INTERMEDIATE CODE: R150 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20150914 Year of fee payment: 3 |
|
| LAPS | Cancellation because of no payment of annual fees |