JPS5959866A - Prehardened material for metallic mold for casting metal with high melting point - Google Patents
Prehardened material for metallic mold for casting metal with high melting pointInfo
- Publication number
- JPS5959866A JPS5959866A JP17053982A JP17053982A JPS5959866A JP S5959866 A JPS5959866 A JP S5959866A JP 17053982 A JP17053982 A JP 17053982A JP 17053982 A JP17053982 A JP 17053982A JP S5959866 A JPS5959866 A JP S5959866A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- melting point
- prehardened
- mold
- quenching
- 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.)
- Granted
Links
Landscapes
- Mold Materials And Core Materials (AREA)
- Heat Treatment Of Nonferrous Metals Or Alloys (AREA)
Abstract
Description
【発明の詳細な説明】
本発明はＦｅ、Ｏｕ系合金など高融点金属鋳造用の金型
材料に適したＱｕ −Ｎｉ−８ｉ系プリハードン型拐料
に関するものである。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a Qu-Ni-8i prehardened mold material suitable as a mold material for casting high-melting point metals such as Fe and O alloys.
高温のＦｅ、Ｏｕ系合金溶湯等の金型鋳造においては大
きな熱衝撃による薄肉部を主体としたヒートクラック、
突起部の溶損、温度勾配による熱応力と強度とのバラン
スに関連した金型の反り、湯道部の溶損、へたり、型締
め圧力によるへたりなどが大きな問題点である。In mold casting of high-temperature Fe and O alloy molten metals, heat cracks mainly occur in thin-walled parts due to large thermal shocks.
Major problems include melting damage to protrusions, warping of molds related to the balance between thermal stress and strength due to temperature gradients, melting damage and sagging of runners, and sagging due to mold clamping pressure.
Ｊ工Ｓ ＳＫＤ６１（５０ｒ−Ｍｏ −■１ｉ１４ ）
など一般の熱間工具材料を使用しても熱伝導率が小さく
、局部的な再焼入効果を受けた場合の過大な硬さ上昇に
よる割れ等のため要求される使用性能を満すことか困難
な場合がある。J Engineering S SKD61 (50r-Mo-■1i14)
Even when using general hot tool materials such as these, the thermal conductivity is low, and cracks may occur due to an excessive increase in hardness when subjected to localized re-hardening effects, so it may not be possible to meet the required usage performance. It can be difficult.
・一方熱伝導率の大きい純銅系材料を使用すれば熱応力
の低減には役立つが、強度か低く型締め圧力によるへた
り、溶損等により長寿命を得ることが困難であり、また
金型の補修溶接が現実的には本可能−Ｃあり、金型材料
としての適用が困難であった。・On the other hand, using pure copper-based materials with high thermal conductivity helps reduce thermal stress, but it is difficult to obtain a long life due to low strength and wear and tear due to mold clamping pressure. In reality, repair welding is only possible, and it is difficult to apply it as a mold material.
本発゛明はＮｉ−８ｉ析出強化型Ｏｕ合金として知られ
るＯｕ −Ｎｉ−Ｓｉ系合金を適切な成分範囲、熱処理
状態の組合せで高融点金机鋳造用金型材料として適用し
、型締め圧力に耐え、熱衝撃によるヒートクラックや大
割れ、熱応力による反りやまた湯道部や金型突起部の溶
損作用に耐え、また湯道部の過冷による湯まわり不良を
まねくことなく、良好な型寿命と成形作業性、溶接補修
性をもたらすことを見出したことにもとすくもので、新
しい高融点金属鋳造用ブリヘードン金型材料を提供する
ものである。The present invention applies an Ou-Ni-Si alloy, known as a Ni-8i precipitation-strengthened Ou alloy, as a mold material for high-melting point metal casting by combining appropriate composition ranges and heat treatment conditions, and It can withstand heat cracks and large cracks caused by thermal shock, warping caused by thermal stress, and erosion of the runners and mold protrusions, and does not cause poor water flow due to overcooling of the runners. We are also pleased to have discovered that this material provides long mold life, molding workability, and welding repairability, and provides a new Brihedon mold material for casting high-melting point metals.
第１表に本発明材料の成分例および焼入温１９００Ｃよ
り各種冷却速度で焼入冷却後、５ｏｏＵｘ２ｂ時効硬化
処理した場合の硬さ、熱伝導率を示す。Table 1 shows examples of the components of the materials of the present invention and the hardness and thermal conductivity when the materials were quenched and cooled at various cooling rates from a quenching temperature of 1900C, and then subjected to 5ooUx2b age hardening treatment.
焼入冷却速度の低下にしたがって０硬さは減少する。The zero hardness decreases as the quenching cooling rate decreases.
本用途の金型材料として必要な硬さＨＲＯ１５以上を確
保するための限界の焼入冷却速度は半冷時間３０ｍ１ｎ
の冷却速度である。The critical quenching cooling rate to ensure the hardness HRO15 or higher required for the mold material for this purpose is half-cooling time of 30 m1n.
cooling rate.
第２表に本発明材料のグ［張試験における硬さと延性を
示す。Table 2 shows the hardness and ductility of the materials of the present invention in the tensile test.
ＨＢＯ３２を越える硬さに熱処理すると延性の低下をま
ねく。Heat treatment to a hardness exceeding HBO32 leads to a decrease in ductility.
第３表に本発明材料の熱伝導率を示す。Table 3 shows the thermal conductivity of the materials of the present invention.
第 ３ 表
本願発明材料は純銅Ｇよりも熱伝導率は低いがたとえは
熱間工具鋼、ｙＸＢＳｘＤ６１の０．０７と比較して明
らかに高いレベルにある。Table 3 The thermal conductivity of the materials of the present invention is lower than that of pure copper G, but it is clearly at a higher level than that of hot work tool steel, yXBSxD61, which is 0.07.
第４表に本願発明材料の耐ヒートクラツク試験結果を示
す。試験片は３０１１ｓφＸ２０ ｍ１挨、３０１１１
φ面をガスバーナで加熱後（試料人の表面温度で５００
Ｃに管理）水冷する操作を２０００回繰返えし、クラツ
ク発生状況３０綿φ面の中央１５闘切断面の表面部クラ
ック個数を観察し、また表面の凹凸状況を観察した。Table 4 shows the heat crack resistance test results of the materials of the present invention. The test piece is 3011sφX20m1, 30111
After heating the φ surface with a gas burner (500% at the sample person's surface temperature)
C) The water cooling operation was repeated 2000 times, and the number of cracks on the surface of the center 15 cut surface of the φ30 cotton φ surface was observed, and the unevenness of the surface was also observed.
第 ４ 表
本発明材料は表面凹凸を生ぜず、またヒートクラックも
試料Ｂに若子みとめられる程度で良好である。比較材料
Ｅは熱伝導率が相対的に低いため表面部の昇温か大きく
、凹凸を生成し、比較材料Ｇはヒートクラックは生じな
かったが強度が低いためやや凹凸を生じた。Table 4 The materials of the present invention do not cause surface irregularities, and heat cracks are good, with only a few visible in sample B. Comparative material E had a relatively low thermal conductivity, so the temperature rise on the surface was large, causing unevenness, and comparative material G did not cause heat cracks, but due to its low strength, some unevenness occurred.
第５表に本願発明材料の耐溶損性試験結果を示す。試験
片は３０ｆｌφ（１４朋φ）×１ＯＯｊＩＩｌｔの円筒
状箱 ５ 表
試料で、１．６５０ ｔ：’で溶解した１８−８ステン
レス鍋の溶湯を繰返えし２０００回高速で円筒内面を通
過させた場合の内径面の最大溶損深さを測定した結果を
示す。本発明材料は比較材料よりも溶損寸法が小さいこ
とがわかる。Table 5 shows the results of the erosion resistance test for the materials of the present invention. The test piece was a cylindrical box of 30flφ (14mmφ) x 1OOjIIlt.5 The molten metal in an 18-8 stainless steel pot melted at 1.650 t:' was passed through the inner surface of the cylinder at high speed 2000 times. The results of measuring the maximum depth of erosion on the inner diameter surface are shown below. It can be seen that the material of the present invention has a smaller erosion loss dimension than the comparative material.
これは熱伝導性と強度とを兼備していることによるもの
である。This is because it has both thermal conductivity and strength.
一方比較材料ｌは熱伝導率が低く、内径面の昇温か大き
いため、また比較材料Ｇは強度が低いため溶損が相対的
に大きく進んだものである。On the other hand, comparative material I has a low thermal conductivity and a large increase in temperature on the inner diameter surface, and comparative material G has low strength, so the melting loss has progressed relatively greatly.
第６表に本願発明材料の溶接性を示す。Table 6 shows the weldability of the materials of the present invention.
溶接方法は１００朋φ×５０−のブロック試験片に１５
ｓＩｊｌφ×１０都深さのくほみをつけ、４５０ｉ：”
に予熱後Ｔｉｇ溶接により各とも材溶接を行なったもの
である。The welding method was to weld 15 mm to a 100mmφ x 50mm block test piece.
Add sIjlφ×10 depth, 450i:”
Each material was welded by TIG welding after preheating.
本発明材料は溶接肉盛可能であり、断面観察でも内部欠
陥等はみとめられなかった。The material of the present invention can be overlaid by welding, and no internal defects were observed even in cross-sectional observation.
比較材料Ｇは熱伝導性がとくに大きいため溶接部の昇温
か行なわれにくく正常な肉盛か田面１となったものであ
る。Comparative material G has particularly high thermal conductivity, so it is difficult to heat up the welded part, resulting in a normal build-up or surface 1.
限 つぎに本発明材料の成分５Ｊ！定理由についてのべる。Limited Next, component 5J of the material of the present invention! Describe the reasons for the decision.
Ｎｉ、Ｓｉは固溶化処理により基地に固浴し、時効処理
によりＮｉ−８ｉ金金属化合物を析出し、本願発明材料
としての必要な強度、熱伝導性、これに関連して耐ヒー
トクラツク性、耐溶損性、溶接性、耐型締めへたり性な
どを付与するために添加する。Ni and Si are solid-bathed in the matrix by solution treatment, and Ni-8i gold metal compound is precipitated by aging treatment, which provides the necessary strength and thermal conductivity as the material of the present invention, as well as related heat crack resistance and melting resistance. Added to provide properties such as breakage resistance, weldability, and resistance to mold clamping.
多ずき゛るど熱伝導率を過度に低下させ、また、低ずき
゛ると上記添加の効果が得られないのでＮ１は２５０〜
８００％、Ｓｉ０．４０％〜ａ００％をする。Ｎｉ 、
Ｓｉのより望ましい範囲はＮ１３．ＯＯ〜６．００％、
Ｓｉα８０〜１５０％である。N1 should be between 250 and 250.
800%, Si 0.40% to a00%. Ni,
A more desirable range of Si is N13. OO~6.00%,
Siα is 80 to 150%.
熱処理は固溶化処理温度として８５０〜９５０Ｃに管理
し、結晶粒の粗大化、溶融相の生成を防色焼人冷却速度
は過大な残留応力の生成を防ぐため、寸法形状等に応じ
、半冷時間３０ｍ１ｎの冷却よりはやい冷油
却文度範囲内にコントロールを行ない、時効処理温度は
本発明材料としての強度を得るために４００〜５５０Ｃ
の範囲であることが必要である。半冷時間３０ｍ１．ｎ
の冷却より遅い冷却速度では本用途の金型として必要な
ＨＲＯ１５以上の強度が得かたくなり、また、一方硬さ
が高すき゛ると被切削性の減少、靭性の減少をともなう
のでＨＲＯ３２以下とする。The heat treatment is controlled at a solution treatment temperature of 850 to 950C to prevent coarsening of crystal grains and the formation of a molten phase.The cooling rate is set to half-cooling depending on the size and shape, etc., in order to prevent the formation of excessive residual stress. The cooling oil temperature is controlled within the temperature range, which is faster than the cooling time of 30 m1n, and the aging treatment temperature is 400 to 550 C to obtain the strength of the material of the present invention.
It is necessary to be within the range of . Half cooling time 30ml1. n
If the cooling rate is slower than the cooling rate, it will be difficult to obtain a strength of HRO15 or higher, which is required for the mold for this purpose.On the other hand, if the hardness is too high, the machinability will decrease and the toughness will decrease, so the HRO should be 32 or lower.
以上の通り、本願発明材料はＮｉ−３ｊ、金属間化合物
の析出による強化を利用したＯｕ −Ｎｉ−８ｉ糸材料
において、高融点金属鋳造用金型材料として必要な耐ヒ
ートクラツク性、強度、延性、耐溶損性、溶接性を伺与
するだめの成分バランス、熱処理の適切な組合せを検討
の結果得られたプリハードン金族材料で辣切削性も良好
で、金型に加工後そのまま使用δわ、良好な金型毒命と
成形ライフル時間の短縮による成形能塾白土に寄令する
ものである。As described above, the material of the present invention is a Ni-3j, Ou-Ni-8i yarn material that utilizes reinforcement by precipitation of intermetallic compounds, and has the heat crack resistance, strength, ductility, and This is a pre-hardened metal material obtained through consideration of the appropriate combination of corrosion resistance, weldability, and heat treatment, and has good sharp machinability. This is due to the mold life and the shortening of the molding rifle time.
代理人 出 中 寿 徳 ′ 、 １Representative Toshi Toku' , 1
Claims (1)
０％、残部Ｏｕよりなる鍛造または鋳造合金を固溶化処
理温度８５０〜９５０Ｃより半冷時間３０ｍ１ｎの冷却
よりはやい冷却速度で焼入冷却ののち、４００〜５５０
Ｃの温度で時効硬化処理し、ＨＨＯ１５〜３２の硬さに
した高融点金属鋳造用プリハルトン金型材料。 Ｚ Ｎｉ３．ＯＯ〜６．００％、Ｓｉ０．８０−１．
５０％、残部Ｏｕよりなる特許請求の範囲第１項記載の
高融点金属鋳造用ブリハードン金型材料。[Claims] 1. Ni2.50~&OO%, Si0.40-40
After quenching and cooling a forged or cast alloy consisting of 0% and the remainder O at a solution treatment temperature of 850 to 950C and a half-cooling time of 30ml at a faster cooling rate,
A pre-Harton mold material for casting high-melting point metals that has been subjected to age hardening treatment at a temperature of C and has a hardness of HHO 15 to 32. Z Ni3. OO~6.00%, Si0.80-1.
5. A brihardon mold material for casting high-melting point metals according to claim 1, comprising 50% and the balance O.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP17053982A JPS5959866A (en) | 1982-09-29 | 1982-09-29 | Prehardened material for metallic mold for casting metal with high melting point |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP17053982A JPS5959866A (en) | 1982-09-29 | 1982-09-29 | Prehardened material for metallic mold for casting metal with high melting point |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS5959866A true JPS5959866A (en) | 1984-04-05 |
| JPS6358219B2 JPS6358219B2 (en) | 1988-11-15 |
Family
ID=15906779
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP17053982A Granted JPS5959866A (en) | 1982-09-29 | 1982-09-29 | Prehardened material for metallic mold for casting metal with high melting point |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS5959866A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5675883A (en) * | 1994-04-29 | 1997-10-14 | Diehl Gmbh & Co. | Method of manufacturing a copper-nickel-silicon alloy casing |
-
1982
- 1982-09-29 JP JP17053982A patent/JPS5959866A/en active Granted
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5675883A (en) * | 1994-04-29 | 1997-10-14 | Diehl Gmbh & Co. | Method of manufacturing a copper-nickel-silicon alloy casing |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS6358219B2 (en) | 1988-11-15 |
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