JPH04339538A - Production of mold for precision casting - Google Patents
Production of mold for precision castingInfo
- Publication number
- JPH04339538A JPH04339538A JP3111534A JP11153491A JPH04339538A JP H04339538 A JPH04339538 A JP H04339538A JP 3111534 A JP3111534 A JP 3111534A JP 11153491 A JP11153491 A JP 11153491A JP H04339538 A JPH04339538 A JP H04339538A
- Authority
- JP
- Japan
- Prior art keywords
- filler
- mold
- fine
- manufacturing
- precision casting
- 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.)
- Pending
Links
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 23
- 238000005495 investment casting Methods 0.000 title claims abstract description 21
- 239000000945 filler Substances 0.000 claims abstract description 54
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 claims abstract description 22
- 229910052593 corundum Inorganic materials 0.000 claims abstract description 20
- 229910001845 yogo sapphire Inorganic materials 0.000 claims abstract description 20
- 239000002002 slurry Substances 0.000 claims abstract description 15
- 239000002245 particle Substances 0.000 claims description 63
- 238000000034 method Methods 0.000 claims description 18
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 claims description 14
- CPLXHLVBOLITMK-UHFFFAOYSA-N Magnesium oxide Chemical compound [Mg]=O CPLXHLVBOLITMK-UHFFFAOYSA-N 0.000 claims description 6
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N Titan oxide Chemical compound O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 claims description 6
- QDOXWKRWXJOMAK-UHFFFAOYSA-N dichromium trioxide Chemical compound O=[Cr]O[Cr]=O QDOXWKRWXJOMAK-UHFFFAOYSA-N 0.000 claims description 6
- ODINCKMPIJJUCX-UHFFFAOYSA-N calcium oxide Inorganic materials [Ca]=O ODINCKMPIJJUCX-UHFFFAOYSA-N 0.000 claims description 3
- 239000010419 fine particle Substances 0.000 claims description 3
- RUDFQVOCFDJEEF-UHFFFAOYSA-N yttrium(III) oxide Inorganic materials [O-2].[O-2].[O-2].[Y+3].[Y+3] RUDFQVOCFDJEEF-UHFFFAOYSA-N 0.000 claims description 3
- MRELNEQAGSRDBK-UHFFFAOYSA-N lanthanum oxide Inorganic materials [O-2].[O-2].[O-2].[La+3].[La+3] MRELNEQAGSRDBK-UHFFFAOYSA-N 0.000 claims description 2
- KTUFCUMIWABKDW-UHFFFAOYSA-N oxo(oxolanthaniooxy)lanthanum Chemical compound O=[La]O[La]=O KTUFCUMIWABKDW-UHFFFAOYSA-N 0.000 claims description 2
- 238000005266 casting Methods 0.000 abstract description 10
- 239000013078 crystal Substances 0.000 abstract description 9
- 239000006255 coating slurry Substances 0.000 abstract 1
- 239000000463 material Substances 0.000 description 12
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 10
- 230000001186 cumulative effect Effects 0.000 description 8
- 238000007711 solidification Methods 0.000 description 7
- 230000008023 solidification Effects 0.000 description 7
- 230000000694 effects Effects 0.000 description 5
- BYFGZMCJNACEKR-UHFFFAOYSA-N aluminium(i) oxide Chemical compound [Al]O[Al] BYFGZMCJNACEKR-UHFFFAOYSA-N 0.000 description 4
- 150000002500 ions Chemical class 0.000 description 4
- 239000000377 silicon dioxide Substances 0.000 description 4
- 229910052681 coesite Inorganic materials 0.000 description 3
- 229910052906 cristobalite Inorganic materials 0.000 description 3
- 238000009792 diffusion process Methods 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 239000011819 refractory material Substances 0.000 description 3
- 235000012239 silicon dioxide Nutrition 0.000 description 3
- 229910052682 stishovite Inorganic materials 0.000 description 3
- 229910052905 tridymite Inorganic materials 0.000 description 3
- 229910052845 zircon Inorganic materials 0.000 description 3
- GFQYVLUOOAAOGM-UHFFFAOYSA-N zirconium(iv) silicate Chemical compound [Zr+4].[O-][Si]([O-])([O-])[O-] GFQYVLUOOAAOGM-UHFFFAOYSA-N 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 239000000919 ceramic Substances 0.000 description 2
- 239000008119 colloidal silica Substances 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- KZHJGOXRZJKJNY-UHFFFAOYSA-N dioxosilane;oxo(oxoalumanyloxy)alumane Chemical compound O=[Si]=O.O=[Si]=O.O=[Al]O[Al]=O.O=[Al]O[Al]=O.O=[Al]O[Al]=O KZHJGOXRZJKJNY-UHFFFAOYSA-N 0.000 description 2
- 229910052863 mullite Inorganic materials 0.000 description 2
- 238000010248 power generation Methods 0.000 description 2
- QVQLCTNNEUAWMS-UHFFFAOYSA-N barium oxide Inorganic materials [Ba]=O QVQLCTNNEUAWMS-UHFFFAOYSA-N 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- CETPSERCERDGAM-UHFFFAOYSA-N ceric oxide Chemical compound O=[Ce]=O CETPSERCERDGAM-UHFFFAOYSA-N 0.000 description 1
- 229910000422 cerium(IV) oxide Inorganic materials 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- CJNBYAVZURUTKZ-UHFFFAOYSA-N hafnium(IV) oxide Inorganic materials O=[Hf]=O CJNBYAVZURUTKZ-UHFFFAOYSA-N 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 238000013001 point bending Methods 0.000 description 1
Landscapes
- Mold Materials And Core Materials (AREA)
- Molds, Cores, And Manufacturing Methods Thereof (AREA)
- Compositions Of Oxide Ceramics (AREA)
Abstract
Description
【０００１】0001
【産業上の利用分野】本発明は、精密鋳造用鋳型の製造
方法に係り、特に発電用ガスタービン設備に設けられる
一方向凝固もしくは単結晶動翼を精密鋳造するのに好適
な、高強度セラミックからなる精密鋳造用鋳型の製造方
法に関するものである。[Industrial Application Field] The present invention relates to a method for manufacturing a precision casting mold, and in particular, a high-strength ceramic suitable for precision casting of unidirectionally solidified or single-crystal rotor blades installed in gas turbine equipment for power generation. The present invention relates to a method for manufacturing a precision casting mold comprising:
【０００２】0002
【従来の技術】従来、ガスタービン用初段動翼には、ク
リープ強度等高温強度に優れた超耐熱合金より成る精密
鋳造品が適用されていた。その鋳型材は、鋳込み温度及
び時間がそれぞれ１４００℃乃至１５００℃、１０分乃
至２０分である普通鋳造において、適性な高温特性を有
するＺｒＯ２系粒子（ＺｒＯ２・ＳｉＯ２）がフィラー
に、またスタッコと呼ばれる細粒耐火物材にはムライト
（３Ａｌ２Ｏ３，２ＳｉＯ２）が適用されていた。しか
し近年、ガスタービンの発電効率を改善するためガス温
度を約１５００℃に高めた高温ガスタービンプラントが
計画されている。2. Description of the Related Art Conventionally, precision castings made of super heat-resistant alloys with excellent high-temperature strength such as creep strength have been used for first-stage rotor blades for gas turbines. The mold material is made of ZrO2-based particles (ZrO2/SiO2), which have suitable high-temperature properties, as a filler and is also called stucco in normal casting where the casting temperature and time are 1400°C to 1500°C and 10 to 20 minutes, respectively. Mullite (3Al2O3, 2SiO2) was used as the fine-grained refractory material. However, in recent years, high-temperature gas turbine plants are being planned in which the gas temperature is increased to approximately 1500° C. in order to improve the power generation efficiency of gas turbines.
【０００３】このガスタービン動翼材料には、高温強度
を高めるため、従来の普通鋳造により製造された多結晶
材料に代えて、結晶の成長方向が遠心応力の発生方向に
一致した一方向凝固材料もしくは、結晶粒界を含まない
、単結晶材料を適用する必要がある。一方向凝固及び単
結晶のための鋳込み条件は、普通鋳造に比べ、高温でか
つ長時間になるため、鋳込み時の鋳型変形の抑制及び溶
湯と鋳型材との反応を防止するため、従来鋳型に比べさ
らに高温強度に優れた鋳型を適用する必要がある。In order to increase the high-temperature strength of this gas turbine rotor blade material, instead of the conventional polycrystalline material manufactured by normal casting, a unidirectionally solidified material whose crystal growth direction coincides with the direction of centrifugal stress generation is used. Alternatively, it is necessary to apply a single crystal material that does not contain grain boundaries. The casting conditions for unidirectional solidification and single crystal are higher temperatures and longer times than normal casting, so in order to suppress mold deformation during casting and prevent reaction between the molten metal and mold material, conventional molds were used. It is necessary to use a mold with even better high-temperature strength.
【０００４】上記の要求に対応する鋳型としては、特開
昭５１−１１９６１６号公報に記載されたように、内側
構成要素がアルミナとシリカ、外側構成要素がジルコン
よりなる高強度鋳型や、特開昭６１−４６３４６号公報
に記載されたように、Ａｌ２Ｏ３粒子とコロイダルシリ
カで構成されるスラリーとＺｒＯ２細粒耐火物とを、交
互にくりかえして塗布した鋳型及びその製造法が提案さ
れている。Molds that meet the above requirements include a high-strength mold whose inner components are made of alumina and silica and whose outer components are made of zircon, as described in JP-A-51-119616; As described in Japanese Patent No. 61-46346, a mold in which a slurry composed of Al2O3 particles and colloidal silica and a ZrO2 fine-grain refractory are alternately applied and a method for manufacturing the same have been proposed.
【０００５】[0005]
【発明が解決しようとする課題】前記従来技術は、高温
強度を改善するため耐熱性に優れた材料を鋳型材に適用
したものである。しかし、スラリー中のフィラーの粒子
径が高温強度に大きな影響を及ぼす点を考慮していない
ため、十分な強度が得られないばかりでなく、粘度特性
等他の性質を損うことが懸念される。強度を補うには、
鋳型の厚さを増すことが効果的であるが、熱伝導性が低
下するため所定の一方向凝固及び単結晶化が得られない
点にも問題があった。[Problems to be Solved by the Invention] In the above-mentioned prior art, a material with excellent heat resistance is applied to the mold material in order to improve high-temperature strength. However, this does not take into account the fact that the particle size of the filler in the slurry has a large effect on high-temperature strength, so there is concern that not only will sufficient strength not be obtained, but other properties such as viscosity characteristics will be impaired. . To add strength,
Although it is effective to increase the thickness of the mold, there is also a problem in that the desired unidirectional solidification and single crystallization cannot be achieved due to a decrease in thermal conductivity.
【０００６】本発明は上記の点に鑑みてなされたもので
あり、粘度特性及び熱伝導性などの鋳型特性を損わずに
高温強度を改善し、一方向凝固及び単結晶鋳物の精密鋳
造性に優れた精密鋳造用鋳型の製造方法を提供すること
を目的とする。The present invention has been made in view of the above points, and aims to improve high temperature strength without impairing mold properties such as viscosity properties and thermal conductivity, and improve unidirectional solidification and precision castability of single crystal castings. The purpose of the present invention is to provide a method of manufacturing an excellent precision casting mold.
【０００７】[0007]
【課題を解決するための手段】上記目的を達成するため
に、本発明はスラリーと細粒耐火物とを交互に塗布する
ことにより、複数層で形成される精密鋳造用鋳型の製造
方法において、前記スラリー中のフィラー及び前記細粒
耐火物が主としてＡｌ２Ｏ３微細粒子よりなり、第１層
中に含まれる前記フィラーの最大粒子径を第２層以降中
に含まれる前記フィラーの最大粒子径より小さくし、か
つ第２層以降中に含まれる前記フィラーの最大粒子径が
１０μｍ以上２００μｍ以下で、平均粒子径が２０μｍ
以上となるようにしたことを特徴としている。[Means for Solving the Problems] In order to achieve the above object, the present invention provides a method for manufacturing a precision casting mold formed in multiple layers by alternately applying a slurry and a fine-grained refractory. The filler in the slurry and the fine refractory are mainly composed of Al2O3 fine particles, and the maximum particle size of the filler contained in the first layer is smaller than the maximum particle size of the filler contained in the second and subsequent layers. , and the maximum particle size of the filler contained in the second and subsequent layers is 10 μm or more and 200 μm or less, and the average particle size is 20 μm.
The present invention is characterized by the following.
【０００８】また、第１層中に含まれるフィラーの最大
粒子径が１００μｍ以下で、平均粒子径が２０μｍ以下
となるようにするとよい。[0008] Further, it is preferable that the maximum particle diameter of the filler contained in the first layer is 100 μm or less, and the average particle diameter is 20 μm or less.
【０００９】さらに、第２層以降中に含まれるフィラー
の最大粒子径及び平均粒子径の少くとも一方を、鋳型の
外側ほど大きくしてもよい。Furthermore, at least one of the maximum particle diameter and the average particle diameter of the filler contained in the second and subsequent layers may be made larger toward the outside of the mold.
【００１０】また、細粒耐火物の平均粒子径に対するフ
ィラーの平均粒子径の比が５％乃至５０％となるように
するとよい。[0010] Furthermore, it is preferable that the ratio of the average particle diameter of the filler to the average particle diameter of the fine-grained refractory is 5% to 50%.
【００１１】一方、本発明の他の発明は、スラリーと細
粒耐火物とを交互に塗布することにより、複数層で形成
される精密鋳造用鋳型の製造方法において、前記スラリ
ー中のフィラー及び前記細粒耐火物が主としてＡｌ２Ｏ
３微細粒子よりなり、前記細粒耐火物の平均粒子径に対
する前記フィラーの平均粒子径の比が５％乃至５０％と
なるようにしたことを特徴としている。On the other hand, another invention of the present invention provides a method for manufacturing a precision casting mold formed in multiple layers by alternately applying a slurry and a fine-grained refractory. Fine-grained refractories are mainly Al2O
The present invention is characterized in that the ratio of the average particle diameter of the filler to the average particle diameter of the fine refractory is 5% to 50%.
【００１２】また、フィラー及び細粒耐火物の少くとも
一方を、Ａｌ２Ｏ３，ＴｉＯ２，ＭｇＯ，ＺｒＯ２，Ｈ
ｆＯ２，Ｙ２Ｏ３，ＣａＯ，Ｌａ２Ｏ３，ＣｅＯ３，Ｃ
ｅＯ２，ＢａＯ及びＣｒ２Ｏ３のうち少くとも１種で構
成してもよい。[0012] Furthermore, at least one of the filler and the fine refractory can be made of Al2O3, TiO2, MgO, ZrO2, H
fO2, Y2O3, CaO, La2O3, CeO3, C
It may be composed of at least one of eO2, BaO and Cr2O3.
【００１３】[0013]
【作用】上記の方法によると、第１層のフィラーの粒子
径を小さくすることにより鋳肌が良好となる。また、第
２層以降のスラリー中に含まれるフィラーの５０％累積
重量に相当する平均粒子径を２０μｍ以上とすることに
より、高温強度が向上する。特に、平均粒子径を３０〜
１００μｍとするのがよい。[Operation] According to the above method, the casting surface is improved by reducing the particle size of the filler in the first layer. Moreover, high temperature strength is improved by setting the average particle diameter corresponding to 50% cumulative weight of the filler contained in the slurry from the second layer onward to 20 μm or more. In particular, the average particle diameter is 30~
The thickness is preferably 100 μm.
【００１４】また、フィラーの粒子径を溶湯側の第１層
から外側へ向かうほど大きくすることにより、曲げ応力
が第１層から外層に向かって圧縮から引張に変化するの
に対応して、各層の鋳型強度を向上することができる。[0014] Furthermore, by increasing the particle size of the filler from the first layer on the molten metal side toward the outside, each layer is The strength of the mold can be improved.
【００１５】さらに、細粒耐火物の平均粒子径に対する
フィラーの平均粒子径の比を一定範囲に限定することに
より、鋳型の密度を高め内部の空隙を減少させ、強度を
向上させることができる。また、第１層及び第２層以降
に用いるフィラーの最大粒子径をそれぞれ１００μｍ以
下及び１００μｍ以上２００μｍ以下とすることによっ
ても同様の効果が得られる。Furthermore, by limiting the ratio of the average particle diameter of the filler to the average particle diameter of the fine-grained refractory to a certain range, it is possible to increase the density of the mold, reduce internal voids, and improve strength. Further, the same effect can be obtained by setting the maximum particle size of the filler used in the first layer and the second layer to 100 μm or less and 100 μm to 200 μm, respectively.
【００１６】一方、鋳型材料をＡｌ２Ｏ３，ＴｉＯ２，
ＭｇＯ，ＺｒＯ２，ＨｆＯ２，Ｙ２Ｏ３，ＣａＯ，Ｌａ
２Ｏ３，ＣｅＯ３，ＣｅＯ２，ＢａＯ及びＣｒ２Ｏ３の
うち少くとも１種で構成することにより、鋳型の強度を
向上するとともに、鋳型材と溶湯との反応を抑制するこ
とができる。On the other hand, the mold material is Al2O3, TiO2,
MgO, ZrO2, HfO2, Y2O3, CaO, La
By comprising at least one of 2O3, CeO3, CeO2, BaO, and Cr2O3, the strength of the mold can be improved and the reaction between the mold material and the molten metal can be suppressed.
【００１７】[0017]
【実施例】以下、本発明の実施例を図１，２及び表１を
参照して説明する。EXAMPLES Examples of the present invention will be described below with reference to FIGS. 1 and 2 and Table 1.
【００１８】表１に作製した各鋳型の構成とそのクリー
プ強度（定常クリープ速度）との関係を示す。Table 1 shows the relationship between the structure of each mold and its creep strength (steady creep rate).
【００１９】[0019]
【表１】[Table 1]
【００２０】上記の表において、Ａ，Ｂ及びＣの５０％
累積重量に相当する平均粒子径は図２に示すようにそれ
ぞれ１４μｍ、１５μｍ及び２０μｍである。また、鋳
型Ｎｏ１乃至Ｎｏ５は本発明による鋳型であり、Ｎｏ６
及びＮｏ７は比較のため作成した鋳型である。In the above table, 50% of A, B and C
The average particle diameters corresponding to the cumulative weight are 14 μm, 15 μm, and 20 μm, respectively, as shown in FIG. Further, molds No. 1 to No. 5 are molds according to the present invention, and No. 6 is a mold according to the present invention.
and No. 7 are molds created for comparison.
【００２１】鋳型Ｎｏ１はフィラーと細粒耐火物の両方
にＡｌ２Ｏ３を用いた。フィラーとして第１層にはＡを
第２層以降にはＣを用い、コロイダルシリカ系のバイン
ダーと混合しスラリーを作製した。その配合割合は第１
層で約８０重量％、粘度は約８００ｃＰであった。Mold No. 1 used Al2O3 for both the filler and the fine refractory. As fillers, A was used for the first layer and C was used for the second and subsequent layers, and these were mixed with a colloidal silica binder to prepare a slurry. The blending ratio is the first
The layer was about 80% by weight and the viscosity was about 800 cP.
【００２２】ここで鋳型の作製手順を説明する。ワック
ス模型を上記のスラリー中に浸漬した後、細粒耐火物を
散布し乾燥を約１時間行ない第１層を形成した。２層以
降のスラリーには前記のフィラーＣを用い、第１層と同
様の工程にてサンディングを繰返し鋳型を作製した。そ
の後、加熱炉内で焼成処理をし所定の特性を具備させた
。焼成は１５５０℃で約３０分保持させ実施した。なお
、細粒耐火物とフィラーとの粒子径の比（５０％累積重
量に相当する粒子径）は、第１層で約９、２層以降で最
大約３７であった。[0022] Here, the procedure for producing the mold will be explained. After the wax model was immersed in the above slurry, a fine refractory material was sprinkled on it and dried for about 1 hour to form a first layer. The filler C described above was used for the slurry for the second and subsequent layers, and a mold was produced by repeating sanding in the same process as for the first layer. Thereafter, it was fired in a heating furnace to provide the desired properties. Firing was carried out by holding the temperature at 1550°C for about 30 minutes. The ratio of the particle diameters of the fine refractory to the filler (particle diameter corresponding to 50% cumulative weight) was about 9 in the first layer, and a maximum of about 37 in the second and subsequent layers.
【００２３】鋳型Ｎｏ２は、フィラーと細粒耐火物にそ
れぞれＡｌ２Ｏ３粒子を用い作製した。使用したフィラ
ー用Ａｌ２Ｏ３粒子は第１層乃至第３層がＡ、それ以降
はＣであった。その作製手順は鋳型Ｎｏ１に示す方法を
用いた。Mold No. 2 was prepared using Al2O3 particles for the filler and the fine refractory. The filler Al2O3 particles used were A for the first to third layers, and C for the subsequent layers. The manufacturing procedure used the method shown in template No.1.
【００２４】鋳型Ｎｏ３は、フィラーと細粒耐火物にそ
れぞれにＡｌ２Ｏ３粒子を用い作成した。第２，３層用
フィラーにＢを用いた点を除き鋳型Ｎｏ２と同様の手順
に従って作成した発明鋳型である。Mold No. 3 was prepared using Al2O3 particles for the filler and the fine refractory. This is an invention mold made according to the same procedure as mold No. 2 except that B was used as the filler for the second and third layers.
【００２５】鋳型Ｎｏ４のフィラー及び細粒耐火物には
それぞれＡｌ２Ｏ３粒子を用いた。このうち、第１〜３
層にはＢを、それ以降にはＣを使用した。フィラーの粒
子径に対する細粒耐火物の粒子径の比（５０％累積重量
に相当する粒子径）は第１層が約８、それ以降の層にお
いて最大３７であった。その作製手順は鋳型Ｎｏ１に用
いた方法と同一であった。[0025] Al2O3 particles were used for the filler and fine refractory of mold No. 4, respectively. Of these, 1st to 3rd
B was used in the layer and C was used thereafter. The ratio of the particle size of the fine refractory to the filler particle size (particle size corresponding to 50% cumulative weight) was about 8 in the first layer and a maximum of 37 in the subsequent layers. The manufacturing procedure was the same as that used for template No.1.
【００２６】鋳型Ｎｏ５のフィラー及び細粒耐火物には
、それぞれＡｌ２Ｏ３及びムライト（３Ａｌ２Ｏ３、２
ＳｉＯ２）を用いた。このうち、フィラー用Ａｌ２Ｏ３
粒子として第１層にはＢを第２層以降にはＣを使用した
。その作製方法は鋳型Ｎｏ４と同一であった。[0026] The filler and fine grain refractory of mold No. 5 contain Al2O3 and mullite (3Al2O3, 2
SiO2) was used. Among these, Al2O3 for filler
As particles, B was used in the first layer, and C was used in the second and subsequent layers. The manufacturing method was the same as mold No.4.
【００２７】次に鋳型Ｎｏ６及びＮｏ７の作製方法を示
す。
鋳型Ｎｏ６にはフィラー及び細粒耐火物としてＡｌ２Ｏ
３粒子を用いた。しかし、用いたＡｌ２Ｏ３粒子は各層
とも５０％累積重量に相当する粒子径が２０μｍ以下で
あるＡを使用した。なお、その作製手順は鋳型Ｎｏ１と
同様であった。鋳型Ｎｏ７はＮｏ６に対し第２層以降に
Ｂを適用した点を特徴とする。しかし、Ｎｏ６と同様、
第２層以降のフィラーの粒子径（５０％累積重量に相当
する粒子径）は２０μｍ以下であった。Next, the method for producing molds No. 6 and No. 7 will be described. Mold No. 6 contains Al2O as filler and fine grain refractory.
Three particles were used. However, the Al2O3 particles used in each layer were A whose particle diameter corresponding to 50% cumulative weight was 20 μm or less. Note that the manufacturing procedure was the same as that for mold No. 1. Mold No. 7 is different from No. 6 in that B is applied to the second and subsequent layers. However, like No. 6,
The particle diameter of the filler in the second layer and subsequent layers (particle diameter corresponding to 50% cumulative weight) was 20 μm or less.
【００２８】以上説明した鋳型Ｎｏ１〜７の高温強度（
定常クリ−プ速度）を表１にまとめて示す。試験は４点
曲げクリ−プ法により、温度１５００℃応力２．５ＭＰ
ａ一定のもとで実施した。第２層以降のフィラーに粒子
径（５０％累積重量に相当する粒子径）２０μｍ以上の
Ｃを用いた本発明鋳型に対しＡ及びＢを用いた比較鋳型
の定常クリ−プ速度は約２〜３倍大きな値を示した。従
来の精密鋳造用鋳型として一般的に用いられているジル
コン（ＺｒＯ２・ＳｉＯ２）系鋳型の強度は、今回比較
のために用いた従来のＡｌ２Ｏ３系鋳型である鋳型Ｎｏ
６に対し使用条件で比較し約１／１００である。そして
、一方向凝固及び単結晶ガスタ−ビン動翼を精密鋳造す
るために必要な鋳型の強度は、凝固時間の関係からジル
コン系鋳型の２００倍以上必要と考えられる。[0028] High-temperature strength of molds No. 1 to 7 explained above (
Steady-state creep rate) are summarized in Table 1. The test was conducted using the 4-point bending creep method at a temperature of 1500℃ and a stress of 2.5MP.
Conducted under constant a. The steady creep rate of the comparative molds using A and B was about 2 to It showed a value 3 times larger. The strength of the zircon (ZrO2/SiO2) mold, which is commonly used as a conventional precision casting mold, is that of mold No. 2, which is a conventional Al2O3 mold used for comparison.
It is about 1/100 compared to 6 under the usage conditions. The strength of the mold required for unidirectional solidification and precision casting of single-crystal gas turbine rotor blades is thought to be 200 times or more stronger than that of a zircon mold due to the solidification time.
【００２９】図１にＡｌ２Ｏ３フィラーを用いた鋳型の
１５００℃におけるクリープ定常速度（クリ−プ強度）
とフィラーの５０％累積重量に相当する粒子径との関係
を示す。クリープ強度は粒子径の増加とともに著しく増
加する。その理由は、アルミナ鋳型のクリープはＡｌの
イオンとＯのイオンが拡散によって移動するためである
ことが明らかとなった。それぞれのイオンの移動する経
路として粒界と粒内が考えられる。本鋳型の場合、拡散
の経路は粒内に比べ粒界が支配的であり変形の速度は粒
子径の２乗に逆比例することがわかった。さらに、フィ
ラーと細粒耐火物のうち、特にフィラーの粒子径が変形
に影響を及ぼすことも明らかとなった。以上の通り、鋳
型の高温変形はＡｌ及びＯイオンの拡散により発生する
。
そのため、鋳型の強度は特にフィラーの粒子径を増加さ
せることにより著しく向上できる。また、その効果は、
フィラーの平均的粒子径を増加させる方法によって有効
に作用する。Figure 1 shows the creep steady rate (creep strength) at 1500°C of a mold using Al2O3 filler.
The relationship between the particle diameter and the particle diameter corresponding to 50% cumulative weight of the filler is shown. Creep strength increases significantly with increasing particle size. It has become clear that the reason for this is that the creep of the alumina template is due to movement of Al ions and O ions due to diffusion. Grain boundaries and grain interiors can be considered as paths through which each ion moves. In the case of this mold, the diffusion path was found to be more dominant at the grain boundaries than within the grains, and the rate of deformation was found to be inversely proportional to the square of the grain size. Furthermore, it has also become clear that the particle size of the filler, especially between the filler and the fine-grained refractory, has an effect on deformation. As described above, high-temperature deformation of the mold occurs due to the diffusion of Al and O ions. Therefore, the strength of the mold can be significantly improved, especially by increasing the particle size of the filler. In addition, the effect is
It works effectively by increasing the average particle size of the filler.
【００３０】本実施例によれば、従来のＡｌ２Ｏ３系鋳
型の強度に比べ約２倍乃至３倍の高強度を得ることがで
き、一方向凝固及び単結晶動翼の精密鋳造用鋳型として
好適である。さらに、Ａｌ２Ｏ３を始めとする各セラミ
ックスは、Ｎｉ基合金溶湯との反応も少ないことから、
この点でも鋳型材として優れた特性を有する。また、第
１層のフィラーの粒子径を小さくすることにより鋳肌を
良好にすることができる。さらに鋳型の第１層から連続
的にフィラーの粒子径を増加させることにより、曲げ応
力が第１層から外層に向って圧縮から引張りに変化する
のに対応した鋳型強度を各層に与えることができる。[0030] According to this example, it is possible to obtain a strength approximately two to three times higher than that of a conventional Al2O3 mold, and it is suitable as a mold for unidirectional solidification and precision casting of single crystal rotor blades. be. Furthermore, since various ceramics including Al2O3 have little reaction with molten Ni-based alloys,
In this respect as well, it has excellent properties as a mold material. Furthermore, by reducing the particle size of the filler in the first layer, the casting surface can be improved. Furthermore, by continuously increasing the particle size of the filler from the first layer of the mold, it is possible to give each layer mold strength that corresponds to the bending stress changing from compression to tension from the first layer to the outer layer. .
【００３１】[0031]
【発明の効果】以上説明したように、本発明によれば、
鋳型材に用いられるスラリー中のフィラーの粒子径（５
０％累積重量に相当する粒子径）を第２層以降に対し約
２０μｍ以上とすることにより、高温強度を約２〜３倍
向上できる。したがって、一方向凝固及び単結晶ガスタ
−ビン動翼を精密鋳造する鋳型の製造方法として効果が
ある。[Effects of the Invention] As explained above, according to the present invention,
Particle size of filler in slurry used for mold material (5
By setting the particle diameter (corresponding to 0% cumulative weight) to about 20 μm or more for the second and subsequent layers, the high temperature strength can be improved about 2 to 3 times. Therefore, it is effective as a method for manufacturing a mold for precision casting of unidirectional solidification and single crystal gas turbine rotor blades.
【図１】フィラーの平均粒子径とクリープ定常速度との
関係を示す線図である。FIG. 1 is a diagram showing the relationship between the average particle diameter of a filler and the steady-state creep rate.
【図２】フィラーの粒子径分布を示す線図である。FIG. 2 is a diagram showing the particle size distribution of filler.
Claims (6)
することにより、複数層で形成される精密鋳造用鋳型の
製造方法において、前記スラリー中のフィラー及び前記
細粒耐火物が主としてＡｌ２Ｏ３微細粒子よりなり、第
１層中に含まれる前記フィラーの最大粒子径を第２層以
降中に含まれる前記フィラーの最大粒子径より小さくし
、かつ第２層以降中に含まれる前記フィラーの最大粒子
径が１０μｍ以上２００μｍ以下で、平均粒子径が２０
μｍ以上となるようにしたことを特徴とする精密鋳造用
鋳型の製造方法。1. A method for manufacturing a precision casting mold formed in multiple layers by alternately applying a slurry and a fine-grained refractory, wherein the filler in the slurry and the fine-grained refractory are mainly Al2O3 fine particles. particles, the maximum particle size of the filler contained in the first layer is smaller than the maximum particle size of the filler contained in the second layer and subsequent layers, and the maximum particle size of the filler contained in the second layer and subsequent layers. The diameter is 10 μm or more and 200 μm or less, and the average particle size is 20 μm or more.
A method for manufacturing a precision casting mold, characterized in that the mold is made to have a diameter of μm or more.
子径が１００μｍ以下で、平均粒子径が２０μｍ以下と
なるようにしたことを特徴とする請求項１記載の精密鋳
造用鋳型の製造方法。2. The method for manufacturing a precision casting mold according to claim 1, wherein the filler contained in the first layer has a maximum particle size of 100 μm or less and an average particle size of 20 μm or less. .
大粒子径及び平均粒子径の少くとも一方を、鋳型の外側
ほど大きくしたことを特徴とする請求項１または２記載
の精密鋳造用鋳型の製造方法。3. The precision casting mold according to claim 1 or 2, wherein at least one of the maximum particle diameter and the average particle diameter of the filler contained in the second and subsequent layers is made larger toward the outside of the mold. manufacturing method.
ラーの平均粒子径の比が５％乃至５０％となるようにし
たことを特徴とする請求項１，２または３記載の精密鋳
造用鋳型の製造方法。4. The precision casting mold according to claim 1, wherein the ratio of the average particle diameter of the filler to the average particle diameter of the fine-grained refractory is 5% to 50%. manufacturing method.
することにより、複数層で形成される精密鋳造用鋳型の
製造方法において、前記スラリー中のフィラー及び前記
細粒耐火物が主としてＡｌ２Ｏ３微細粒子よりなり、前
記細粒耐火物の平均粒子径に対する前記フィラーの平均
粒子径の比が５％乃至５０％となるようにしたことを特
徴とする精密鋳造用鋳型の製造方法。5. A method for manufacturing a precision casting mold formed in multiple layers by alternately applying a slurry and a fine-grained refractory, wherein the filler in the slurry and the fine-grained refractory are mainly Al2O3 fine particles. A method for manufacturing a precision casting mold, characterized in that the ratio of the average particle diameter of the filler to the average particle diameter of the fine-grained refractory is 5% to 50%.
方が、Ａｌ２Ｏ３，ＴｉＯ２，ＭｇＯ，ＺｒＯ２，Ｈｆ
Ｏ２，Ｙ２Ｏ３，ＣａＯ，Ｌａ２Ｏ３，ＣｅＯ３，Ｃｅ
Ｏ２，ＢａＯ及びＣｒ２Ｏ３のうち少くとも１種で構成
されることを特徴とする請求項１，２，３，４または５
記載の精密鋳造用鋳型の製造方法。6. At least one of the filler and the fine refractory contains Al2O3, TiO2, MgO, ZrO2, Hf
O2, Y2O3, CaO, La2O3, CeO3, Ce
Claim 1, 2, 3, 4 or 5, characterized in that it is composed of at least one of O2, BaO and Cr2O3.
A method for manufacturing the precision casting mold described above.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3111534A JPH04339538A (en) | 1991-05-16 | 1991-05-16 | Production of mold for precision casting |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3111534A JPH04339538A (en) | 1991-05-16 | 1991-05-16 | Production of mold for precision casting |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH04339538A true JPH04339538A (en) | 1992-11-26 |
Family
ID=14563789
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3111534A Pending JPH04339538A (en) | 1991-05-16 | 1991-05-16 | Production of mold for precision casting |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH04339538A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2012525260A (en) * | 2009-04-30 | 2012-10-22 | エボニック デグサ ゲーエムベーハー | Dispersion, slurry, and method for producing casting mold for precision casting using the slurry |
-
1991
- 1991-05-16 JP JP3111534A patent/JPH04339538A/en active Pending
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2012525260A (en) * | 2009-04-30 | 2012-10-22 | エボニック デグサ ゲーエムベーハー | Dispersion, slurry, and method for producing casting mold for precision casting using the slurry |
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