JPWO2013035351A1 - Alloy composition for aluminum die-cast mold and method for producing the same - Google Patents
Alloy composition for aluminum die-cast mold and method for producing the same Download PDFInfo
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- 229910052782 aluminium Inorganic materials 0.000 title claims abstract description 55
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title claims abstract description 55
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 47
- 239000000956 alloy Substances 0.000 title claims abstract description 47
- 239000000203 mixture Substances 0.000 title claims abstract description 23
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 9
- 238000004512 die casting Methods 0.000 claims abstract description 22
- 229910052742 iron Inorganic materials 0.000 claims abstract description 13
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 7
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 6
- 239000013078 crystal Substances 0.000 claims abstract description 6
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 6
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 6
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 6
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 5
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 4
- 230000001590 oxidative effect Effects 0.000 claims abstract description 3
- 229910001182 Mo alloy Inorganic materials 0.000 abstract description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 17
- 230000003647 oxidation Effects 0.000 description 16
- 238000007254 oxidation reaction Methods 0.000 description 16
- 238000000034 method Methods 0.000 description 9
- 239000000463 material Substances 0.000 description 7
- 229910052751 metal Inorganic materials 0.000 description 7
- 239000002184 metal Substances 0.000 description 7
- 238000002844 melting Methods 0.000 description 6
- 230000008018 melting Effects 0.000 description 6
- 229910000838 Al alloy Inorganic materials 0.000 description 5
- 229910000831 Steel Inorganic materials 0.000 description 4
- 239000000919 ceramic Substances 0.000 description 4
- 230000009257 reactivity Effects 0.000 description 4
- 239000010959 steel Substances 0.000 description 4
- 229910000990 Ni alloy Inorganic materials 0.000 description 3
- 238000002441 X-ray diffraction Methods 0.000 description 3
- 238000002347 injection Methods 0.000 description 3
- 239000007924 injection Substances 0.000 description 3
- 150000002736 metal compounds Chemical class 0.000 description 3
- 238000007796 conventional method Methods 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 238000004381 surface treatment Methods 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 1
- 229910018594 Si-Cu Inorganic materials 0.000 description 1
- 229910008465 Si—Cu Inorganic materials 0.000 description 1
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000000151 deposition Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 229910052749 magnesium Inorganic materials 0.000 description 1
- 239000011777 magnesium Substances 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
- 238000007751 thermal spraying Methods 0.000 description 1
- MTPVUVINMAGMJL-UHFFFAOYSA-N trimethyl(1,1,2,2,2-pentafluoroethyl)silane Chemical compound C[Si](C)(C)C(F)(F)C(F)(F)F MTPVUVINMAGMJL-UHFFFAOYSA-N 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 239000011701 zinc Substances 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/07—Alloys based on nickel or cobalt based on cobalt
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22C—FOUNDRY MOULDING
- B22C9/00—Moulds or cores; Moulding processes
- B22C9/06—Permanent moulds for shaped castings
- B22C9/061—Materials which make up the mould
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D17/00—Pressure die casting or injection die casting, i.e. casting in which the metal is forced into a mould under high pressure
- B22D17/20—Accessories: Details
- B22D17/22—Dies; Die plates; Die supports; Cooling equipment for dies; Accessories for loosening and ejecting castings from dies
- B22D17/2209—Selection of die materials
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
Abstract
６０〜７０重量％のＣｏと、２５〜３３重量％のＣｒと、４〜７重量％のＭｏと、残部がＳｉ、Ｍｎ、Ｆｅ、Ｚｒ、Ｃ、Ｎ、及び／又は不可避的不純物から成るＣｏ−Ｃｒ−Ｍｏ系合金を、大気中で、温度６００〜９００℃で、０．５〜５時間保持し、その表面を酸化して製造され、ｆｃｃのγ相、ｈｃｐのε相、またはそれらの混晶相から成る、アルミニウムダイキャスト金型用合金組成物およびその製造方法。Co consisting of 60-70 wt% Co, 25-33 wt% Cr, 4-7 wt% Mo, the balance consisting of Si, Mn, Fe, Zr, C, N and / or inevitable impurities A Cr—Mo alloy is produced by holding the surface at 600 to 900 ° C. in the atmosphere for 0.5 to 5 hours and oxidizing the surface thereof, fcc γ phase, hcp ε phase, or those The alloy composition for aluminum die-casting molds which consists of a mixed crystal phase, and its manufacturing method.
Description
本発明は、アルミニウムの溶湯との反応性が低い、アルミダイキャスト製品の金型材料として好適な、アルミニウムダイキャスト金型用合金組成物およびその製造方法に関するものである。 The present invention relates to an alloy composition for an aluminum die-casting mold that has low reactivity with molten aluminum and is suitable as a mold material for an aluminum die-casting product, and a method for producing the same.
従来、アルミニウムダイキャスト（以下、アルミダイキャストとも記す）の金型用の材料としては、高温引張強さに優れた、ＪＩＳ ＳＫＤ６１の様な特殊鋼が一般的に使用されている。しかしながら、従来の鉄を主成分とする金型材料は、アルミニウムの溶湯との反応性が高く、特にアルミニウムの溶湯との接触時間が長い、金型のスリーブ部において、鉄成分がアルミニウムの溶湯と反応し、金属間化合物となり、結果的に、金型材料がアルミニウムの溶湯に溶け出すという現象が発生し、短時間の使用で、金型が使用できなくなり、金型を頻繁に交換する必要があるという問題点があった。 Conventionally, a special steel such as JIS SKD61, which is excellent in high-temperature tensile strength, is generally used as a die material for aluminum die-casting (hereinafter also referred to as aluminum die-casting). However, the conventional mold material mainly composed of iron has high reactivity with the molten aluminum, and in particular, the contact portion with the molten aluminum has a long contact time with the molten aluminum alloy. It reacts and becomes an intermetallic compound. As a result, the phenomenon that the mold material melts into the molten aluminum occurs, the mold cannot be used in a short time, and the mold needs to be replaced frequently. There was a problem that there was.
金型の鉄成分がアルミニウムの溶湯に溶け出すのを防止する方法としては、金型のアルミニウムの溶湯の接触部にセラミックスを蒸着する方法があるが、セラミックスと金型との熱膨脹係数の違いから、セラミックス層が剥離してしまい、顕著な効果が得られていない。 As a method of preventing the iron component of the mold from melting into the molten aluminum, there is a method of depositing ceramics at the contact portion of the molten aluminum of the mold, but due to the difference in thermal expansion coefficient between the ceramic and the mold. The ceramic layer peels off, and a remarkable effect is not obtained.
また、金型の鉄成分がアルミニウムの溶湯に溶け出すのを防止する方法として、接触面にニッケル合金層を溶射で形成した後、ニッケル合金層に炭化チタンを真空高温雰囲気で埋め込む方法が提案されているが、製造プロセスが複雑で、高コストになるので実用的ではない（例えば、特許文献１参照）。 Also, as a method to prevent the iron component of the mold from melting into the molten aluminum, a method is proposed in which a nickel alloy layer is formed on the contact surface by thermal spraying and then titanium carbide is embedded in the nickel alloy layer in a vacuum high temperature atmosphere. However, since the manufacturing process is complicated and expensive, it is not practical (see, for example, Patent Document 1).
更に、金型の鉄成分がアルミニウムの溶湯に溶け出すのを防止する方法として、セラミックス製の内側管とそれに嵌合した鋼材製の外側管とから構成され、外側管の内側にニッケル合金層を形成したアルミニウム給湯管の提案もあるが、勘合部に高い寸法精度が要求され、高コストになるので実用的ではない（例えば、特許文献２参照）。 Furthermore, as a method for preventing the iron component of the mold from melting into the molten aluminum, it is composed of a ceramic inner tube and a steel outer tube fitted thereto, and a nickel alloy layer is formed inside the outer tube. Although there is also a proposal for a formed aluminum hot water pipe, it is not practical because a high dimensional accuracy is required for the fitting portion and the cost is high (for example, see Patent Document 2).
そこで、本発明は、このような課題に着目してなされたもので、原材料費としては、鉄系合金よりやや高いが、金型寿命が長く、その結果、金型交換回数が少なくなるような、アルミニウム溶湯との反応性が低いＣｏ−Ｃｒ−Ｍｏ系合金を使用して、その化学組成を最適化し、更に、表面処理でアルミニウム溶湯に溶けない組成物を表面に形成したアルミニウムダイキャスト金型用合金組成物およびその製造方法を提供することを目的としている。 Therefore, the present invention has been made paying attention to such problems, and the raw material cost is slightly higher than that of the iron-based alloy, but the mold life is long, and as a result, the number of times of mold replacement is reduced. An aluminum die-cast mold using a Co—Cr—Mo alloy with low reactivity with molten aluminum, optimizing its chemical composition, and further forming a composition on the surface that is not soluble in molten aluminum by surface treatment It is an object of the present invention to provide an alloy composition and a method for producing the same.
本発明によれば、６０〜７０重量％のＣｏと、２５〜３３重量％のＣｒと、４〜７重量％のＭｏと、残部がＳｉ、Ｍｎ、Ｆｅ、Ｚｒ、Ｃ、Ｎ、および／または不可避的不純物から成ることを特徴とするアルミニウムダイキャスト金型用合金組成物が得られる。Ｓｉ、Ｍｎ、Ｆｅ、Ｚｒ、Ｃ、Ｎ、および／または不可避的不純物は、１重量％未満であることが好ましい。 According to the present invention, 60 to 70 wt% Co, 25 to 33 wt% Cr, 4 to 7 wt% Mo, the balance being Si, Mn, Fe, Zr, C, N, and / or An alloy composition for an aluminum die-casting mold characterized by comprising inevitable impurities is obtained. Si, Mn, Fe, Zr, C, N, and / or inevitable impurities are preferably less than 1% by weight.
また、本発明によれば、ｆｃｃのγ相、ｈｃｐのε相、またはそれらの混晶相から成ることを特徴とするアルミニウムダイキャスト金型用合金組成物が得られる。 In addition, according to the present invention, there can be obtained an alloy composition for an aluminum die-cast mold, comprising an fcc γ phase, an hcp ε phase, or a mixed crystal phase thereof.
さらに、本発明によれば、６０〜７０重量％のＣｏと、２５〜３３重量％のＣｒと、４〜７重量％のＭｏと、残部がＳｉ、Ｍｎ、Ｆｅ、Ｚｒ、Ｃ、Ｎ、および／または不可避的不純物から成るＣｏ−Ｃｒ−Ｍｏ系合金を、大気中で、温度６００〜９００℃で、０．５〜５時間保持することにより、その表面を酸化させることを特徴とするアルミニウムダイキャスト金型用合金組成物の製造方法が得られる。 Furthermore, according to the present invention, 60-70 wt% Co, 25-33 wt% Cr, 4-7 wt% Mo, the balance being Si, Mn, Fe, Zr, C, N, and An aluminum die characterized in that the surface thereof is oxidized by holding a Co—Cr—Mo alloy composed of inevitable impurities in the atmosphere at a temperature of 600 to 900 ° C. for 0.5 to 5 hours. A method for producing an alloy composition for cast molds is obtained.
本発明によれば、原材料費としては、鉄系合金よりやや高いが、金型寿命が長く、その結果、金型交換回数が少なくなるような、アルミニウム溶湯との反応性が低いＣｏ−Ｃｒ−Ｍｏ系合金を使用して、その化学組成を最適化し、更に、表面処理でアルミニウム溶湯に溶けない組成物を表面に形成したアルミニウムダイキャスト金型用合金組成物およびその製造方法を提供することができる。また、アルミダイカスト用Ｃｏ−Ｃｒ−Ｍｏ系合金は、従来の鉄系合金より耐熱疲労特性に優れているため、この合金を使用して製造されたアルミダイカスト用金型の耐食性を向上させることができる。アルミダイカスト用Ｃｏ−Ｃｒ−Ｍｏ系合金は、アルミニウムダイキャスト金型の他に、亜鉛用、マグネシウム用ダイキャスト金型としても有効である。 According to the present invention, the raw material cost is slightly higher than that of the iron-based alloy, but the mold life is long, and as a result, the number of times of mold replacement is reduced. Co-Cr- having low reactivity with molten aluminum To provide an alloy composition for an aluminum die-casting die, which uses a Mo-based alloy, optimizes its chemical composition, and further forms a composition on the surface that does not dissolve in molten aluminum by surface treatment, and a method for producing the same. it can. In addition, since the Co-Cr-Mo alloy for aluminum die casting has better thermal fatigue characteristics than conventional iron alloys, the corrosion resistance of the die for aluminum die casting produced using this alloy can be improved. it can. The Co—Cr—Mo based alloy for aluminum die casting is effective as a die casting die for zinc and magnesium in addition to an aluminum die casting die.
以下、この発明の実施の形態を図に基づいて説明する。
上記従来技術と本発明の実施の形態との相違点として、従来技術では、ＪＩＳ ＳＫＤ６１の様な特殊鋼が使用され、金型がアルミニウムの溶湯に溶け出すのを防止する方法としては、溶湯との接触部にセラミックスを蒸着する方法や、ニッケル合金層を溶射形成する方法があるが、本発明の実施の形態では、アルミニウムの溶湯と反応容易な鉄を含有しないＣｏ−Ｃｒ−Ｍｏ系合金を使用し、大気中高温酸化処理を実施し、試料表面で均一的な酸化皮膜を形成することにより、金型がアルミニウムの溶湯に溶け出すのを有効的に防止することができる。Embodiments of the present invention will be described below with reference to the drawings.
As a difference between the above-described conventional technique and the embodiment of the present invention, in the conventional technique, a special steel such as JIS SKD61 is used, and a method for preventing the mold from melting into the molten aluminum is as follows. However, in the embodiment of the present invention, a Co—Cr—Mo alloy that does not contain iron that easily reacts with molten aluminum is used. It is possible to effectively prevent the mold from being melted into the molten aluminum by using a high-temperature oxidation treatment in the atmosphere and forming a uniform oxide film on the sample surface.
図１は、本発明の実施の形態によるＣｏ−２９Ｃｒ−６Ｍｏ−０．１４Ｎ系合金を、大気中で、７５０℃、２４時間で高温酸化処理する前後のＸＲＤ（Ｘ線回折）分析結果である。図１に示すように、Ｃｏ−Ｃｒ−Ｍｏ−０．１４Ｎ系合金を相変態点（８５０℃）以下で酸化処理しながら、高温で安定なＦＣＣ結晶構造を持つγ相から、低温安定なＨＣＰ結晶構造のε相への相変態が起きている。表面形成した酸化物は、Ｃｒが主に含まれる（Ｃｒ．Ｍ）２Ｏ３酸化物である。ここで、Ｍは、合金に含まれた他の元素（Ｃｏ，Ｓｉ，Ｍｏなど）である。FIG. 1 is a result of XRD (X-ray diffraction) analysis before and after the Co-29Cr-6Mo-0.14N alloy according to the embodiment of the present invention is subjected to high-temperature oxidation treatment at 750 ° C. for 24 hours in the atmosphere. . As shown in FIG. 1, a low temperature stable HCP is obtained from a γ phase having a FCC crystal structure stable at high temperatures while oxidizing a Co—Cr—Mo—0.14N alloy at a phase transformation point (850 ° C.) or lower. A phase transformation of the crystal structure to the ε phase occurs. The oxide formed on the surface is a (Cr.M) 2 O 3 oxide mainly containing Cr. Here, M is another element (Co, Si, Mo, etc.) contained in the alloy.
図２は、本発明の実施の形態によるＣｏ−Ｃｒ−Ｍｏ−０．１４Ｎ系合金（ＣＣＭ ａｌｌｏｙ）を、７５０℃、２４時間で大気中酸化処理した後の表面組織である。図２に示すように、表面における酸化物が、平均粒径１００〜５００ｎｍで、均一的に形成されていることが確認できる。酸化物皮膜には空孔が見られず、緻密である。７５０℃、２４時間で大気中酸化処理した後は、酸化物被膜（Ｏｘｉｄｅ ｌａｙｅｒ）の厚さが３００〜４００ｎｍレベルになっている。 FIG. 2 is a surface texture after the Co—Cr—Mo—0.14N alloy (CCM alloy) according to the embodiment of the present invention is oxidized in the atmosphere at 750 ° C. for 24 hours. As shown in FIG. 2, it can be confirmed that the oxide on the surface is uniformly formed with an average particle diameter of 100 to 500 nm. The oxide film is dense with no pores. After oxidation in the atmosphere at 750 ° C. for 24 hours, the thickness of the oxide layer is about 300 to 400 nm.
図３は、本発明の実施の形態によるＣｏ−Ｃｒ−Ｍｏ−０．１４Ｎ系合金を、それぞれ６００℃、２４時間（Ｔ６００−２４ｈ）および８００℃、２４時間（Ｔ８００−２４ｈ）で酸化処理を実施した後の表面組織である。図３に示すように、６００℃、２４時間で熱処理した酸化物皮膜（Ｏｘｉｄｅ ｌａｙｅｒ）は、８００℃、２４時間の結果と比べて、表面の欠陥（空孔）が多く、皮膜が薄く、酸化物の結晶粒径が細かくなっている。このことから、高温で酸化処理を実施して、酸化物皮膜の厚さが増加することにより、金型がアルミニウムの溶湯に溶け出すのを一層有効的に防止できると考えられる。 FIG. 3 shows the oxidation treatment of the Co—Cr—Mo—0.14N alloy according to the embodiment of the present invention at 600 ° C., 24 hours (T600-24h) and 800 ° C., 24 hours (T800-24h), respectively. It is the surface texture after the execution. As shown in FIG. 3, the oxide film heat-treated at 600 ° C. for 24 hours has many surface defects (holes), the film is thin, and the oxidation film is thinner than the result at 800 ° C. for 24 hours. The crystal grain size of the product is fine. From this, it is considered that by performing the oxidation treatment at a high temperature and increasing the thickness of the oxide film, it is possible to more effectively prevent the mold from melting into the molten aluminum.
図４は、本発明の実施の形態による、試料表面に異なる粗さを持つＣｏ−Ｃｒ−Ｍｏ−０．１４Ｎ合金を、それぞれ６００℃、２４時間（Ｔ６００−２４ｈ）および８００℃、２４時間（Ｔ８００−２４ｈ）で酸化処理した後の表面組織である。図４に示すように、試料の表面を適度に粗く研磨して酸化処理した試料の方が、酸化物皮膜が均一的に形成されるが、高温（８００℃）で酸化処理した後の試料では、この傾向がはっきり見られない。 FIG. 4 shows a Co—Cr—Mo—0.14N alloy with different roughness on the sample surface, according to an embodiment of the present invention, at 600 ° C., 24 hours (T600-24h) and 800 ° C., 24 hours ( It is a surface texture after oxidation treatment at T800-24h). As shown in FIG. 4, the oxide film is formed more uniformly in the sample that has been subjected to oxidation treatment by moderately roughing the surface of the sample, but in the sample after oxidation treatment at a high temperature (800 ° C.) This trend is not clearly seen.
図５は、未熱処理、および、本発明の実施の形態による７５０℃、２４時間酸化処理後のＣｏ−Ｃｒ−Ｍｏ−０．１４Ｎ合金（厚さ２ｍｍ）を、７２０℃のアルミニウムの溶湯に１時間浸漬した後の断面組織である。また、図６は、それらの試料を７２０℃のアルミニウムの溶湯に浸漬したときの、試料の断面の厚さの時間変化を示している。図５および図６に示すように、未処理試料（Ｕｎｔｒｅａｔｅｄ ｓａｍｐｌｅｓ）では厚さ（Ｘ）が大きく減るが、酸化処理後の試料（Ｔｒｅａｔｅｄ ｓａｍｐｌｅｓ）では厚さの変化がなく、金型がアルミニウムの溶湯に溶け出すのを非常に有効的に防止できている。 FIG. 5 shows that a Co—Cr—Mo—0.14N alloy (thickness: 2 mm) after 750 ° C. and 24 hours oxidation treatment according to an embodiment of the present invention is used as an aluminum melt at 720 ° C. It is a cross-sectional structure after time immersion. Moreover, FIG. 6 shows the time change of the thickness of the cross section of the sample when those samples were immersed in the molten metal of 720 ° C. As shown in FIGS. 5 and 6, the thickness (X) of the untreated sample is greatly reduced, but the thickness of the sample after the oxidation treatment (Treated samples) is not changed, and the mold is made of aluminum. It is very effectively prevented from melting into the molten metal.
図７は、未処理Ｃｏ−Ｃｒ−Ｍｏ−０．１４Ｎ合金を、７２０℃のアルミニウムの溶湯に１時間浸漬した後の断面組織である。図７に示すように、試料の表面とアルミニウムの溶湯とが激しく反応し、Ｃｏ−Ｃｒ−Ｍｏ−０．１４Ｎ合金（ＣＣＭ ａｌｌｏｙ）とアルミニウムの溶湯（Ａｌ）との間にＣｏ−Ｃｒ−Ｍｏ−Ａｌの金属化合物が形成され、アルミニウムの溶湯にＣｒ−ＭｏーＡｌ相が分散されている。そのＣｏ−Ｃｒ−Ｍｏ−Ａｌの金属化合物の組成（ａｔ％）は約８３．５Ａｌ−１０．８６Ｃｏ−４．９４Ｃｒ−０．７１Ｍｏであり、分散されているＣｒ−Ｍｏ−Ａｌ相の組成は、７．１２Ｃｒ−２．２２Ｍｏ−８９．９７Ａｌである。 FIG. 7 shows a cross-sectional structure after immersing an untreated Co—Cr—Mo—0.14N alloy in a molten aluminum at 720 ° C. for 1 hour. As shown in FIG. 7, the surface of the sample and the molten aluminum react vigorously, and the Co—Cr—Mo is formed between the Co—Cr—Mo—0.14N alloy (CCM alloy) and the molten aluminum (Al). A metal compound of -Al is formed, and the Cr-Mo-Al phase is dispersed in the molten aluminum. The composition (at%) of the Co-Cr-Mo-Al metal compound is about 83.5Al-10.86Co-4.94Cr-0.71Mo, and the composition of the dispersed Cr-Mo-Al phase is 7.12Cr-2.22Mo-89.97Al.
図８は、本発明の実施の形態による、７５０℃、２４時間で酸化処理したＣｏ−Ｃｒ−Ｍｏ−０．１４Ｎ合金を、７２０℃のアルミニウムの溶湯に２時間浸漬した後のある断面の組織である。図８に示すように、試料（ＣＣＭ ａｌｌｏｙ）の表面とアルミニウムの溶湯（Ａｌ）との間の酸化物皮膜に破壊が起きると、合金とアルミニウムの溶湯との間に直接的な反応が起き、図７で述べた金属化合物が形成されて膨張が起き、錐体｛すいたい｝の形を持つ組織（ｃｏｎｅ−ｓｈａｐｅｄ ｓｔｒｕｃｔｕｒｅ）が形成されている。 FIG. 8 shows a structure of a cross section after a Co—Cr—Mo—0.14N alloy oxidized at 750 ° C. for 24 hours is immersed in a molten aluminum at 720 ° C. for 2 hours according to an embodiment of the present invention. It is. As shown in FIG. 8, when the oxide film between the surface of the sample (CCM alloy) and the molten aluminum (Al) breaks down, a direct reaction occurs between the alloy and the molten aluminum, The metal compound described in FIG. 7 is formed and expansion occurs, and a cone-shaped structure (cone-shaped structure) is formed.
アルミダイキャストマシン（コールドチャンバマシン）を用いて、ＪＩＳアルミ合金（ＡＤＣ１０ Ａｌ−Ｓｉ−Ｃｕ系合金）の自動車部品（キャブレタ）の製造を行い、溶湯射出装置のスリーブの寿命評価を行った。アルミ合金溶湯射出装置のスリーブ材を、開発合金（Ｃｏ−２９Ｃｒ−６Ｍｏ−０．０５Ｃ−０．０５Ｚｒ−０．１４Ｎ合金）で作製した。また、比較として、ＪＩＳ ＳＫＤ６１鋼を用いてアルミ合金溶湯射出装置のスリーブ材を試作した。アルミ合金の溶湯は７００℃であった。結果として、ＳＫＤ６１製のスリーブは、３５，０００ショットの使用で亀裂が生じたが、開発合金のスリーブは３８０，０００回のショットでも使用可能な状態であった。このことから、開発合金は、アルミダイキャスト用スルーブ材料として優れていることが判明した。
Using an aluminum die-casting machine (cold chamber machine), JIS aluminum alloy (ADC10 Al—Si—Cu-based alloy) automobile parts (carburetors) were manufactured, and the life evaluation of the sleeve of the molten metal injection device was performed. The sleeve material of the aluminum alloy molten metal injection device was made of the developed alloy (Co-29Cr-6Mo-0.05C-0.05Zr-0.14N alloy). For comparison, a sleeve material for an aluminum alloy molten metal injection device was manufactured using JIS SKD61 steel. The molten aluminum alloy was 700 ° C. As a result, the SKD61 sleeve cracked after 35,000 shots, but the developed alloy sleeve was usable even after 380,000 shots. From this, it was found that the developed alloy is excellent as a through material for aluminum die casting.
Claims (3)
Co consisting of 60-70 wt% Co, 25-33 wt% Cr, 4-7 wt% Mo, the balance consisting of Si, Mn, Fe, Zr, C, N and / or inevitable impurities An alloy composition for an aluminum die-casting mold characterized by oxidizing a surface of a Cr—Mo-based alloy by holding it in the atmosphere at a temperature of 600 to 900 ° C. for 0.5 to 5 hours. Production method.
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| JP2004269994A (en) * | 2003-03-11 | 2004-09-30 | Japan Science & Technology Agency | BIOCOMPATIBLE Co BASED ALLOY, AND PRODUCTION METHOD THEREFOR |
| JP2006265633A (en) * | 2005-03-24 | 2006-10-05 | Iwate Univ | Co-Cr-Mo ALLOY FOR LIVING BODY FOR DEALING WITH MRI, AND ITS PRODUCTION METHOD |
| JP2008038179A (en) * | 2006-08-03 | 2008-02-21 | Hiroshi Kai | Hot chamber die-casting machine and casting method using it |
| WO2010026996A1 (en) * | 2008-09-05 | 2010-03-11 | 国立大学法人東北大学 | METHOD OF FORMING FINE CRYSTAL GRAINS IN NITROGEN-DOPED Co-Cr-Mo ALLOY AND NITROGEN-DOPED Co-Cr-Mo ALLOY |
| JP2010215960A (en) * | 2009-03-16 | 2010-09-30 | Iwate Univ | Method for producing machine part, and machine part |
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| JP2004269994A (en) * | 2003-03-11 | 2004-09-30 | Japan Science & Technology Agency | BIOCOMPATIBLE Co BASED ALLOY, AND PRODUCTION METHOD THEREFOR |
| JP2006265633A (en) * | 2005-03-24 | 2006-10-05 | Iwate Univ | Co-Cr-Mo ALLOY FOR LIVING BODY FOR DEALING WITH MRI, AND ITS PRODUCTION METHOD |
| JP2008038179A (en) * | 2006-08-03 | 2008-02-21 | Hiroshi Kai | Hot chamber die-casting machine and casting method using it |
| WO2010026996A1 (en) * | 2008-09-05 | 2010-03-11 | 国立大学法人東北大学 | METHOD OF FORMING FINE CRYSTAL GRAINS IN NITROGEN-DOPED Co-Cr-Mo ALLOY AND NITROGEN-DOPED Co-Cr-Mo ALLOY |
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