JPH01157758A - Method for casting nickel aluminum bronze - Google Patents
Method for casting nickel aluminum bronzeInfo
- Publication number
- JPH01157758A JPH01157758A JP31531487A JP31531487A JPH01157758A JP H01157758 A JPH01157758 A JP H01157758A JP 31531487 A JP31531487 A JP 31531487A JP 31531487 A JP31531487 A JP 31531487A JP H01157758 A JPH01157758 A JP H01157758A
- Authority
- JP
- Japan
- Prior art keywords
- mold
- casting
- molten metal
- liquid nitrogen
- temp
- 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
- 238000005266 casting Methods 0.000 title claims abstract description 49
- 229910000906 Bronze Inorganic materials 0.000 title claims abstract description 7
- 239000010974 bronze Substances 0.000 title claims abstract description 7
- KUNSUQLRTQLHQQ-UHFFFAOYSA-N copper tin Chemical compound [Cu].[Sn] KUNSUQLRTQLHQQ-UHFFFAOYSA-N 0.000 title claims abstract description 7
- 238000000034 method Methods 0.000 title claims description 22
- NPXOKRUENSOPAO-UHFFFAOYSA-N Raney nickel Chemical compound [Al].[Ni] NPXOKRUENSOPAO-UHFFFAOYSA-N 0.000 title claims description 5
- 239000002184 metal Substances 0.000 claims abstract description 27
- 229910052751 metal Inorganic materials 0.000 claims abstract description 27
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims abstract description 8
- 230000007547 defect Effects 0.000 claims abstract description 4
- 229910015372 FeAl Inorganic materials 0.000 claims abstract 2
- 239000004576 sand Substances 0.000 abstract description 30
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 abstract description 26
- 238000001816 cooling Methods 0.000 abstract description 19
- 229910000831 Steel Inorganic materials 0.000 abstract description 16
- 239000010959 steel Substances 0.000 abstract description 16
- 229910052757 nitrogen Inorganic materials 0.000 abstract description 14
- 239000007788 liquid Substances 0.000 abstract description 13
- 239000000498 cooling water Substances 0.000 abstract description 11
- 239000000463 material Substances 0.000 abstract description 8
- 229910052759 nickel Inorganic materials 0.000 abstract description 3
- 239000010953 base metal Substances 0.000 abstract description 2
- 229910001005 Ni3Al Inorganic materials 0.000 abstract 1
- 229910052782 aluminium Inorganic materials 0.000 abstract 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 abstract 1
- 238000007664 blowing Methods 0.000 abstract 1
- 230000001376 precipitating effect Effects 0.000 abstract 1
- 238000007670 refining Methods 0.000 abstract 1
- 239000000047 product Substances 0.000 description 9
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 7
- 239000003110 molding sand Substances 0.000 description 4
- 239000002244 precipitate Substances 0.000 description 4
- 239000013535 sea water Substances 0.000 description 4
- 230000007797 corrosion Effects 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 238000007711 solidification Methods 0.000 description 3
- 230000008023 solidification Effects 0.000 description 3
- 101000693961 Trachemys scripta 68 kDa serum albumin Proteins 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 238000007796 conventional method Methods 0.000 description 2
- 238000007872 degassing Methods 0.000 description 2
- 230000003628 erosive effect Effects 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 239000012530 fluid Substances 0.000 description 2
- 238000002347 injection Methods 0.000 description 2
- 239000007924 injection Substances 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 238000007528 sand casting Methods 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 241001676573 Minium Species 0.000 description 1
- 239000004115 Sodium Silicate Substances 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 238000004881 precipitation hardening Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000000926 separation method Methods 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- NTHWMYGWWRZVTN-UHFFFAOYSA-N sodium silicate Chemical compound [Na+].[Na+].[O-][Si]([O-])=O NTHWMYGWWRZVTN-UHFFFAOYSA-N 0.000 description 1
- 229910052911 sodium silicate Inorganic materials 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は舶用ブロベフ、海水ポンプ及び泥水ポンプの羽
根、ケージングなどに使用されるニッケｆｉ１７Ｊ％、
’ミニウム青銅（以下、Ｎ１ＡＬＢ２と略記する）の鋳
造法に関する。[Detailed Description of the Invention] [Industrial Application Field] The present invention is directed to nickel fi 17J%, which is used for marine blobef, seawater pump and mud pump impellers, casings, etc.
'Regarding a casting method for minium bronze (hereinafter abbreviated as N1ALB2).
従来、ＮｉＡｔＢ２鋳物は鋳物砂型法によって製造され
ていた。その態様を第４図によって説明する。第４図の
（ａ）はその斜視図、わ）は断面図を示す。第４図にお
いて１は鋳型（砂型）、２はＮ ｉ ＡＬＢ ２溶湯注
入口、３は鋳型材料、ＡはＮ ｉ ｋｔＢ 、鋳物を示
し、数値は鋳型１及び鋳物人の各寸法（−）を示す。Conventionally, NiAtB2 castings have been manufactured by the foundry sand casting method. The aspect will be explained with reference to FIG. FIG. 4(a) is a perspective view, and FIG. 4(a) is a sectional view. In Fig. 4, 1 indicates the mold (sand mold), 2 indicates the N i ALB 2 molten metal inlet, 3 indicates the mold material, A indicates the N i ktB, and the casting, and the numerical values indicate the dimensions (-) of the mold 1 and the caster. show.
第４図から分るように従来のものは、鋳型材料３として
鋳物砂で対象製品（こ−ではＮ１Ａ−１Ｂｚ鋳物）の鋳
型１を作り、これにＮ ｉ ＡＬＢ７．溶湯を溶湯注入
口２より注湯する。溶湯は鋳型１の中で時間の経過とと
もにゆっくり冷却し鋳物Ａができ上る。As can be seen from FIG. 4, in the conventional method, a mold 1 of the target product (N1A-1Bz casting in this case) is made using molding sand as the mold material 3, and Ni ALB7. The molten metal is poured from the molten metal injection port 2. The molten metal slowly cools down in the mold 1 over time, and a casting A is completed.
その後、鋳物Ａが常温近くになった時点で鋳物砂を取去
シ、即ち、鋳型１を砕いて鋳物人を取出すことになる。Thereafter, when the temperature of the casting A reaches near room temperature, the foundry sand is removed, that is, the mold 1 is crushed and the caster is removed.
表１にＮ ｉ ｋｔＢ ２の化学成分を示す。Table 1 shows the chemical components of NiktB2.
表Ｉ ＮｉＡｔＢ２の化学成分 （％）〔発明が解決
しようとする問題点〕
表１に示すように、Ｎ ｉ ＡｔＢ ２はＣｕの他、Ｎ
ｉ、 ＡＬ、 Ｆｅなどを含む析出硬化型合金である。Table I Chemical components of NiAtB2 (%) [Problems to be solved by the invention] As shown in Table 1, NiAtB2 contains not only Cu but also N
It is a precipitation hardening alloy containing i, AL, Fe, etc.
従って、その機械的性質は、ＦｅＡｔおよびＮｉ３Ａｔ
の析出物の形状によって変化する。そのため、従来のよ
うな断熱効果をもつ鋳物砂の中に溶湯を注湯し、常温近
くまでゆっくりと冷却凝固させる鋳造法の場合、ＦｅＡ
ｔおよびＮｉ５Ａｔの析出物が成長粗大化し、機械的性
質が大幅に低下する。Therefore, its mechanical properties are similar to that of FeAt and Ni3At.
varies depending on the shape of the precipitate. Therefore, in the case of the conventional casting method in which molten metal is poured into molding sand, which has a heat insulating effect, and is slowly cooled and solidified to near room temperature, FeA
The precipitates of t and Ni5At grow and coarsen, and the mechanical properties are significantly reduced.
この機械的性質の低下により、
（１）引張強さや疲労強度（海水中で使用する場合は腐
食疲労強度）が低下するのでこれを補うために鋳物製品
の肉厚を厚くする必要があシ、必要原材料の増加、重量
の増加、加工工数の増加を招く、
（２）材料の硬さが低下することによシ、流体と一緒に
使用する製品（舶用プロペラや水車）の場合、キャビテ
ーシミン、エロージョンが発生しやすい。Due to this decrease in mechanical properties, (1) the tensile strength and fatigue strength (corrosion fatigue strength when used in seawater) decrease, so it is necessary to increase the wall thickness of the cast product to compensate for this; (2) In the case of products used with fluids (marine propellers and water turbines), cavity shimming, Erosion is likely to occur.
本発明はＮ ｉ ＡＡＢ ２鋳物を鋳造する際、ＦｅＡ
ｔおよびＮｉ、Ａｔの析出物の粗大化を防止し、微細析
出物として機械的性質を増加させるには、Ｎ１ＡｔＢｚ
を鋳造後、即ち、溶湯を鋳型に注湯した後、急冷処理を
する必要があることの知見を得た。本発明はこの知見に
基づいて完成したものであって、ニッケルアルミニウム
青銅溶湯の鋳造後に急冷し、Ｎｉ１Ａｔ、 ＦｅＡｔの
介在物を微細化して金属組織内に析出させ、機械的性質
の向上と鋳造欠陥の低減を図ることを特徴とするニッケ
ルアルミニウム青銅の鋳造法である。The present invention uses FeA when casting N i AAB 2 castings.
In order to prevent coarsening of precipitates of t, Ni, and At and to increase mechanical properties as fine precipitates, N1AtBz
It was found that after casting, that is, after pouring the molten metal into the mold, it is necessary to perform a rapid cooling process. The present invention was completed based on this knowledge, and the nickel-aluminum bronze molten metal is rapidly cooled after casting, and Ni1At and FeAt inclusions are made fine and precipitated within the metal structure, thereby improving mechanical properties and eliminating casting defects. This is a method for casting nickel-aluminum bronze, which is characterized by reducing the amount of
本発明方法において、Ｎ ｉ ｋｔＢ ２鋳物の鋳造後
、該鋳物を急冷する具体的手段としては、（１）砂型水
冷法、（２）砂型液体窒素冷却法、（３）砂型剥離空冷
法及び（４）鋼粒鋳造法があげられる。In the method of the present invention, specific means for rapidly cooling the N i ktB 2 casting after casting include (1) sand mold water cooling method, (2) sand mold liquid nitrogen cooling method, (3) sand mold peeling air cooling method, and ( 4) Steel grain casting method is mentioned.
以下、急冷処理を備えた上記４種類の鋳造法と従来の鋳
造法について比較実験を実施した。Hereinafter, a comparative experiment was conducted between the above four types of casting methods including quenching treatment and the conventional casting method.
〔実施例１〕
第１図に従って本発明の一実施例である砂型水冷法の例
を説明する。第１図の（ａ）はその斜視図、ら）は断面
図を示す。第１図において１は鋳型（砂型）、２はＮ
ｉ ＡｔＢ ２溶湯注入口、３は鋳型材料（こ−では鋳
物砂）、４は冷却水管、５は冷却水入口、６は冷却水出
口、７はサーモカップル式温度計、ＡはＮ１ＡＡＢ２鋳
物を示し、数値は鋳型１及び鋳物Ａの各寸法（■）を示
す。な、 お冷却水管４の内径は３０■、全長１２ｍで
ある。[Example 1] An example of a sand mold water cooling method, which is an embodiment of the present invention, will be described with reference to FIG. FIG. 1(a) shows a perspective view, and FIG. 1(a) shows a sectional view. In Figure 1, 1 is a mold (sand mold), 2 is N
i AtB 2 Molten metal inlet, 3 mold material (foundry sand in this case), 4 cooling water pipe, 5 cooling water inlet, 6 cooling water outlet, 7 thermocouple thermometer, A indicates N1AAB2 casting. , numerical values indicate each dimension (■) of mold 1 and casting A. The inner diameter of the cooling water pipe 4 is 30 mm and the total length is 12 m.
第１図に示すように、鋳型１の鋳物砂３の中に冷却水管
４を埋め込んだ。埋め込み位置は鋳物入側面から２５Ｗ
１鋳物Ａ下面から５０−になるようにした。As shown in FIG. 1, a cooling water pipe 4 was embedded in molding sand 3 of a mold 1. The embedding position is 25W from the casting side.
1 Casting A It was made to be 50 - from the bottom surface.
Ｎ ｉ ＡＬＢ ２溶湯を鋳込温度的１１５０℃で溶湯
注入口２より注湯する。温度約１０００℃になるとＮ
ｉ ｋｔＢ 、は凝固するが、この温度をサーモカップ
ル式温度計７で計測し、約１０００℃になった時に、冷
却水管４中に冷却水口５よシ約１９℃の冷却水を１６０
ｔ／分の割合で流して急冷させた。冷却水出口６からの
水の温度は２４℃であった。N i ALB 2 molten metal is poured from the molten metal injection port 2 at a casting temperature of 1150°C. When the temperature reaches about 1000℃, N
i ktB solidifies, but this temperature is measured with a thermocouple thermometer 7, and when it reaches about 1000°C, cooling water of about 19°C is poured into the cooling water pipe 4 through the cooling water port 5 at 160°C.
It was rapidly cooled by flowing at a rate of t/min. The temperature of the water from the cooling water outlet 6 was 24°C.
〔実施例２〕
第２図に従って本発明の一実施例である砂型液体窒素冷
却法の例を説明する。第２図の（ａ）はその斜視図、伽
）は断面図を示す。第２図において、１は鋳型（砂型）
、２はＮ ｉ ｋｔＢ ２溶湯注入口、３は鋳型材料（
こ−では鋳物砂）、７はサーモカップル式温度計、８は
液体窒素ボンベ、９は液体窒素供給鋼管、１０はストッ
プ弁、ＡはＮ１ＡＬＢ２鋳物を示し、数値は鋳型１及び
鋳物人の各寸法（■）を示す。[Example 2] An example of a sand mold liquid nitrogen cooling method, which is an embodiment of the present invention, will be described with reference to FIG. FIG. 2(a) is a perspective view, and FIG. 2(a) is a sectional view. In Figure 2, 1 is a mold (sand mold)
, 2 is Ni ktB 2 molten metal inlet, 3 is mold material (
7 is a thermocouple thermometer, 8 is a liquid nitrogen cylinder, 9 is a liquid nitrogen supply steel pipe, 10 is a stop valve, A is N1ALB2 casting, and the numbers are the dimensions of mold 1 and the caster. (■) indicates.
第２図に示すように、鋳物Ａ側面砂原さ５０雪、鋳物Ａ
下面砂原さ１００日とし、実施例１と同様にＮ ｉ Ａ
ＡＢ ２溶湯を鋳込温度的１１５０℃で溶湯注入口２よ
シ注暢し、溶湯温度が１０００℃（凝固終了温度）にな
ったことをサーモカップル式温度計７で計測し、ストッ
プ弁１０を開にして液体窒素ボンベ８より液体窒素供給
鋼管９を介して液体窒素を鋳型１に吹付けて急冷させた
。As shown in Figure 2, the sandy field on the side of casting A is 50 snow,
The lower surface was exposed to sand for 100 days, and N i A was applied in the same manner as in Example 1.
AB 2 Molten metal is poured into the molten metal inlet 2 at a casting temperature of 1150°C, and the thermocouple thermometer 7 measures when the molten metal temperature reaches 1000°C (solidification completion temperature), and the stop valve 10 is turned on. The mold 1 was opened and liquid nitrogen was blown onto the mold 1 from a liquid nitrogen cylinder 8 through a liquid nitrogen supply steel pipe 9 to rapidly cool it.
〔実施例３〕
第３図に従って本発明の一実施例である悄粒鋳造法の例
を説明する。第３図の（ａ）はその斜視図、（１））は
断面図を示す。第３図にお１ハて、１は、鋳型で、鋳物
Ａに最接近部３！は鋼粒１（５＠而厚さ２０−１下面厚
さ４０鱈）、中間、１３雪は鋼粒と鋳物砂の混合１（側
面厚さ２０■、下面厚さ４０燗）、最外、１ｈは鋳物砂
、１（側面厚さ１０−１下面厚さ２０ ｗｍ ）よりな
るものである。２はＩＪｉＡｔＢ２溶沿注入口、ＡはＮ
ｉＡｔＢ２鋳物を示し、数値は鋳型１の寸法、鋳型１の
材質、１厚さ及び鋳物Ａの寸法（１）を夫々示す。[Embodiment 3] An example of a thin grain casting method, which is an embodiment of the present invention, will be explained with reference to FIG. FIG. 3(a) is a perspective view thereof, and FIG. 3(1)) is a sectional view thereof. In Fig. 3, 1 is the mold, and the part 3 closest to the casting A! is steel grain 1 (5 @ thickness 20-1, bottom thickness 40mm), middle, 13 snow is a mixture of steel grains and foundry sand 1 (side thickness 20cm, bottom thickness 40mm), outermost, 1h is foundry sand made of 1 (side thickness 10-1 bottom surface thickness 20 wm). 2 is IJiAtB2 welding inlet, A is N
The iAtB2 casting is shown, and the numerical values indicate the dimensions of the mold 1, the material of the mold 1, the thickness of the mold 1, and the dimension (1) of the casting A, respectively.
鋼粒Ｗ３ｔの鋼粒は直径約１ｆｉのものを使用し、その
粘結剤としてはケイ酸ソーダを使用した。Steel grains W3t having a diameter of about 1 fi were used, and sodium silicate was used as the binder.
また鋼粒と鋳物砂の混合５１５．は鋼粒と鋳物砂を同容
量ずつ混合したものを使用した。Also, a mixture of steel grains and foundry sand 515. A mixture of equal volumes of steel grains and foundry sand was used.
上記構成の鋳型１に溶湯注入口２より祷込温度約１１５
０℃のＮｉＡｔＢ２溶湯を注入すると、溶湯に接する鋼
粒層３１は鋳物砂に比べてはるかに燥伝導率が高いので
溶湯と鋼粒、す３！の接触面はすぐ冷却凝固するように
なるばかシでなく、鋳物Ａの内部も急冷される。また鋳
造時に発生するガスは鋼粒間を通って外部に抜けるため
ガス抜き性が良好となり、鋳造欠陥である微小鋳巣が激
減する。The temperature of about 115
When NiAtB2 molten metal at 0°C is injected, the steel grain layer 31 in contact with the molten metal has a much higher dry conductivity than foundry sand, so the molten metal and steel grains are separated by 3! The contact surface of the casting A does not immediately cool and solidify, but the inside of the casting A is also rapidly cooled. In addition, the gas generated during casting passes through between the steel grains and escapes to the outside, which improves degassing performance and drastically reduces the number of micro-porosity, which is a casting defect.
〔実施例４〕
本発明の一突施例としては、砂型剥離空冷法があげられ
るが、この方法は従来の鋳物砂型法と同じ鋳型を用い、
Ｎ１ＡｔＢｚ溶湯を注湯後、それが約１０００°Ｃの凝
固終了温度になった時、鋳型の鋳物砂を工具によって除
去し、高温の鋳物を空気に直接々触させて急冷するもの
である。[Example 4] An example of the present invention is the sand mold separation air cooling method, which uses the same mold as the conventional foundry sand mold method,
After pouring the N1AtBz molten metal, when it reaches the final solidification temperature of approximately 1000°C, the molding sand in the mold is removed using a tool, and the hot casting is brought into direct contact with air to be rapidly cooled.
上記の急冷処理を備えた４つの実施例方法と従来の鋳造
法についての比較実験結果を表２に対比して示す。Table 2 shows the results of a comparative experiment between the four embodiment methods provided with the above-mentioned quenching treatment and the conventional casting method.
この表よシ下記のことが分る。This table reveals the following.
（１）本発明の砂型水冷法、砂型液体窒素冷却法、砂型
剥離法、鋼粒鋳型法の機械的性質（引張強さ、伸び、プ
リネル硬さ、海水中腐食疲労強度）は、従来の鋳物砂型
法（余冷法）に比べて優れていること。(1) The mechanical properties (tensile strength, elongation, Prinell hardness, seawater corrosion fatigue strength) of the sand mold water cooling method, sand mold liquid nitrogen cooling method, sand mold peeling method, and steel grain casting method of the present invention are different from those of conventional castings. Superiority compared to the sand mold method (after-cooling method).
特に引張強さや海水中腐食疲労強度の増加は、Ｎ ｉ
ＡｔＢ ２製品の肉厚を従来品よりも薄くでき、必要原
材料（地金）の低減、製品の軽量化、加工工数の低減が
可能となる。In particular, the increase in tensile strength and seawater corrosion fatigue strength is
The wall thickness of AtB 2 products can be made thinner than conventional products, making it possible to reduce the amount of raw materials (base metal) required, the weight of the product, and the number of processing steps.
また、材料の硬さの増加は、流体中で使用すルＮ１Ａｔ
Ｂ７製品の場合、キャビテーション、エロージョンの発
生を抑制する。Also, the increase in hardness of the material is due to the increase in the hardness of the material used in fluids.
In the case of B7 products, cavitation and erosion are suppressed.
（２）鋳物の切断面を観察した結果、本発明の急冷法は
従来法に比べて微小鋳巣が大幅に減少し、鋼粒鋳型では
皆無に近かった。これは、ガス抜き性が良好であったこ
と及び鋳造時の指向性凝固がうまくなされたことを物語
っている。鋳巣の大幅減少は品質向上につながシ、製品
の損傷を少なくするのに貢献する。(2) As a result of observing the cut surface of the casting, the rapid cooling method of the present invention significantly reduced the number of micro-porous cavities compared to the conventional method, and in the case of steel grain molds, there were almost no micro-porous cavities. This indicates that the degassing properties were good and the directional solidification during casting was successful. A significant reduction in blow holes leads to improved quality and contributes to reducing product damage.
本発明の鋳型急冷法（砂型水冷法、砂型液体窒素冷却法
、砂型剥離空冷法、鋼粒鋳型法）は従来の鋳型徐冷法（
鋳物砂型法）Ｋ比べて、下記の効果をもつ。The mold rapid cooling method of the present invention (sand mold water cooling method, sand mold liquid nitrogen cooling method, sand mold peeling air cooling method, steel grain molding method) is different from the conventional mold slow cooling method (
Casting sand mold method) Compared to K, it has the following effects.
（１） 機械的性質が向上するため、Ｎ ｉ ＡＡＢ
２製品の薄肉化、小型化、軽量化、必要地金の低減、
加工工数の低減が可能となシ、耐キャビチー第１図〜第
３図は本発明の詳細な説明するための図であシ、第１図
は砂型水冷法、第２図は砂型液体窒素冷却法、第３図は
鋼粒鋳造法の鋳造例の説明図、第４図は従来の鋳物砂鋳
造法の説明図である。(1) Because the mechanical properties are improved, N i AAB
2. Thinner products, smaller size, lighter weight, and reduced metal requirements.
Figures 1 to 3 are diagrams for explaining the details of the present invention. Figure 1 shows the sand mold water cooling method, and Figure 2 shows the sand mold liquid nitrogen cooling method. Fig. 3 is an explanatory diagram of a casting example of the steel grain casting method, and Fig. 4 is an explanatory diagram of a conventional foundry sand casting method.
Claims (1)
＿３Ａｌ、ＦｅＡｌの介在物を微細化して金属組織内に
析出させ、機械的性質の向上と鋳造欠陥の低減を図るこ
とを特徴とするニツケルアルミニウム青銅の鋳造法。After casting the nickel aluminum bronze molten metal, it is rapidly cooled and Ni
_3 A method for casting nickel aluminum bronze, which is characterized in that inclusions of Al and FeAl are made fine and precipitated within the metal structure to improve mechanical properties and reduce casting defects.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP31531487A JPH01157758A (en) | 1987-12-15 | 1987-12-15 | Method for casting nickel aluminum bronze |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP31531487A JPH01157758A (en) | 1987-12-15 | 1987-12-15 | Method for casting nickel aluminum bronze |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH01157758A true JPH01157758A (en) | 1989-06-21 |
Family
ID=18063908
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP31531487A Pending JPH01157758A (en) | 1987-12-15 | 1987-12-15 | Method for casting nickel aluminum bronze |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH01157758A (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2679161A1 (en) * | 1991-07-19 | 1993-01-22 | Giat Ind Sa | Casting method and mould for improving the fineness of grain of moulded metallic components |
| EP0890400A1 (en) * | 1997-06-17 | 1999-01-13 | Wärtsilä NSD Schweiz AG | Casting method and mould for making metallic mouldings |
| CN101817073A (en) * | 2010-05-14 | 2010-09-01 | 许广和 | Process for manufacturing cadmium plate and cadmium alloy plate |
| CN104607619A (en) * | 2015-02-09 | 2015-05-13 | 曾寿农 | Method for improving overall metal performance |
| EP3539687A1 (en) * | 2017-12-27 | 2019-09-18 | Casa Maristas Azterlan | Device and method for improved cooling of a metallic alloy in a sand mold |
-
1987
- 1987-12-15 JP JP31531487A patent/JPH01157758A/en active Pending
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2679161A1 (en) * | 1991-07-19 | 1993-01-22 | Giat Ind Sa | Casting method and mould for improving the fineness of grain of moulded metallic components |
| EP0890400A1 (en) * | 1997-06-17 | 1999-01-13 | Wärtsilä NSD Schweiz AG | Casting method and mould for making metallic mouldings |
| KR100567360B1 (en) * | 1997-06-17 | 2006-07-03 | 베르트질레 슈바이츠 악티엔게젤샤프트 | Casting method and a casting mould for the manufacture of metallic cast parts |
| CN101817073A (en) * | 2010-05-14 | 2010-09-01 | 许广和 | Process for manufacturing cadmium plate and cadmium alloy plate |
| CN104607619A (en) * | 2015-02-09 | 2015-05-13 | 曾寿农 | Method for improving overall metal performance |
| EP3539687A1 (en) * | 2017-12-27 | 2019-09-18 | Casa Maristas Azterlan | Device and method for improved cooling of a metallic alloy in a sand mold |
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