JP2746878B2 - Plastic molding pre-hardened steel for mold - Google Patents
Plastic molding pre-hardened steel for moldInfo
- Publication number
- JP2746878B2 JP2746878B2 JP62015840A JP1584087A JP2746878B2 JP 2746878 B2 JP2746878 B2 JP 2746878B2 JP 62015840 A JP62015840 A JP 62015840A JP 1584087 A JP1584087 A JP 1584087A JP 2746878 B2 JP2746878 B2 JP 2746878B2
- Authority
- JP
- Japan
- Prior art keywords
- steel
- machinability
- present
- hardness
- polishing
- 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 - Lifetime
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- Moulds For Moulding Plastics Or The Like (AREA)
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明はHRC43ないしこれを越える高い硬さでも極め
て選れた被切削性を有することを特徴とし、かつ優れた
研磨仕上性を兼備した新しいプリハードンタイプのプラ
スチック成形金型用鋼に関するものである。
〔従来の技術〕
高級プラスチック成形金型用鋼としては、
（１）鏡面仕上性が良く、ピンホールやその他微細ピッ
トの発生傾向が小さい、
（２）シボ加工性が良いこと、
（３）耐食、耐発錆性が良いこと、
（４）強度、耐摩耗性、靭性が良いこと、
（５）被切削性が良いこと、
などが要求される。
しかし、近年高硬度化と併せて硬の製作納期の短縮が
特に重要な顧客要求として強く提起されたが、従来のよ
うに被加工性改善のために単にＳなど快削性付与元素を
添加して改善をはかる方式のみではHRC43ないしこれを
越える高い硬さでの優れた被切削性を保持させることが
困難であった。
〔問題点を解決しようとする問題点〕
本発明は、HRC43ないしこれを越える高い硬さで優れ
た被切削性を備え、かつ高硬度とあいまって極めて優れ
た研磨仕上性を備えた合金を提供することを目的とする
ものである。
〔発明が解決するための手段〕
すなわち、本発明鋼は低Ｃ−中〜低Mn−Ni−Mo（Ｗ）
−高Cu−高Al−Ｓ系を基本成分とする合金であり、焼入
により均一な上部ベイナイト組織を生成し、さらに500
℃以上の高温焼もどしにより、低Ｃのベイナイト地にCu
−Fe固溶体、Ni−Al金属間化合物、Mo（Ｗ）炭化物を析
出させ、時効（析出）硬化による高い強度を付与すると
ともに、適度に脆化を起させ、基地自体に極めて良好な
被切削性を付与するとともに、快削性を付与するための
硫化物の分布とあいまって、HRC43ないしこれを越える
高硬度において極めて優れた被切削性を得るとともに優
れた研磨仕上性を保持するものである。また、Cr、Mo、
Ｗ、Cu、Niの含有により優れた耐食性、耐発錆性が得ら
れ、さらに放電加工による硬化が少なく、この点でも仕
上加工が容易である。
本発明鋼は、HRC37ないしそれ以上の硬さのプリハー
ドン状態（一般に焼入後400℃以上の焼もどし）で供給
され、そのまま型彫加工→研磨仕上を施して使用される
もので、HRC43ないしそれ以上でも優れた被切削性を保
持するものである。
したがって、ユーザーでの熱処理を要せず、最高度の
良好な被切削性、高い硬さと均質な基地とがあいまっ
て、極めて優れた研磨仕上性をもたらし、また、へた
り、摩耗の懸念を要せず、長寿命を与えることを可能に
する新しいプラスチック成形金型用鋼である。
〔実施例〕
以下本発明を実施例に基づき説明する。
第１表に本発明鋼の実施例と比較鋼の化学成分を示
す。比較鋼Ｋは快削鋼ではあるが、特に靭性が優れてい
ることを特徴とする型用鋼である。比較鋼Ｌは0.77％の
Alを含有し、被切削性は比較鋼Ｋのそれよりも優れてお
り、適度な靭性を兼備しているが、高Al系の本発明鋼に
対比して被切削性は劣るものである。
第２表に本発明鋼のHRC44に熱処理したもののエンド
ミルによる切削の場合のSCM440（HRC37.5）を基準とし
た被切削性指数および切削面最大アラサ比を示す。 本発明鋼は、HRC44前後の高い硬さ水準においてもSCM
440（HRC37.5）よりも被切削性が格段に優れており、ま
た切削面アラサも格段に細かく、以後の研磨加工の工数
低減に効果が大きいことを示している。
第３表は、本願発明鋼の鏡面仕上性（耐ピット性）を
比較鋼Ｌ、Ｍと対比したものである。
資料は50mm角でHRC44に焼入、焼もどし処理後、グラ
インダー→ペーパー→ダイヤモンドコンパウンド研磨の
方式で鏡面仕上を行ない、10倍の拡大鏡を用いて微細な
ピット発生個数をカウントしたものである。
本発明鋼は硬さが高く、比較鋼Ｌ、Ｍに対比してピッ
ト発生の傾向が小さい。
第４表に本発明鋼の切削加工後の研磨仕上の所要時間
を従来鋼のそれと対比して示した。
試料は50mm×50mmで、熱処理後エンドミルにより切削
加工を行なったのち、砥石→ペーパー→ダイヤモンドコ
ンパウンド研磨の方式で鏡面仕上を行ない、仕上完了ま
での所要時間を比較鋼Ｍのそれを100として指数で示し
たものである。
本願発明鋼は硬さが高く、深い研磨痕を生じず、また
硫化物の分散とあいまって、研磨における切粉の除去が
円滑に行なわれ、優れた研磨仕上性を示す。
次に本発明鋼の成分限定理由について述べる。
Ｃは本発明鋼の焼入組織を被切削性の良好な塊状上部
ベイナイト組織に保ち、かつ焼もどしにおけるCu−Fe固
溶体、Ni−Al金属間化合物及びMo、Ｗ炭化物の析出に基
づく析出硬化をもたらすための基質を与えるための基本
的添加元素である。多すぎると、基地をマルテンサイト
組織化して被切削性を減じ、かつ過度の炭化物を形成し
て被切削性を低下させる。
また、放電加工性を劣化させ、鏡面仕上性を減じ、さ
らに放電硬化性を高め、放電加工後の研磨加工工数の増
加をまねくので0.17％以下とし、低すぎるとフェライト
析出をまねき、かつ十分な焼もどし（時効）硬さが得ら
れないのでAlほかの合金組成との関係において0.08％以
上とする。
Mnは本発明鋼のベイナイト焼入性を高め、またフェラ
イトの生成を抑制し、適度の焼入、焼もどし（時効）硬
さを与えるために添加される。多すぎるとベイナイト変
態温度を低下させ、ベイナイト組織を過度に微細化さ
せ、また基地の粘さを上げて被切削性を低下させるので
1.20％以下とし、低すぎると上記添加の効果が得られな
いので0.50％以上とする。
Siは使用時の雰囲気に対する耐食性を高めるために目
的、用途により添加される。多すぎるとフェライトの生
成をまねき、また被切削性を低下させるので0.60％以下
とする。
Niは本発明鋼のベイナイト焼入性を高め、またフェラ
イトの生成を抑制し、焼もどし（時効）時、Ni−Al金属
間化合物を析出させ、本発明鋼の特徴である高い硬さを
得るとともに、延性を適度に低下させ、被切削性の向上
を得るために添加される。多すぎるとベイナイト変態温
度を低下させ、ベイナイト組織を過度に微細化させ、ま
た基地の粘さを上げて被切削性を低下させるので3.50％
以下とし、低すぎると上記添加の効果が得られないので
2.50％以上とする。
Crは本発明鋼の耐食性、また窒化時の硬さを高め、ま
た研磨加工時あるいは金型保管時の発錆を抑制するた
め、目的、用途により添加される。多すぎるとベイナイ
ト組織を微細化し、特に高い被切削性を狙いとする本願
発明鋼としての特性を維持することが困難となるので0.
50％以下とする。
Ｗ、Moは本発明鋼の500℃を越える高温焼もどし（時
効）処理において微細炭化物を析出し、析出（時効）硬
化をもたらし、本発明鋼の強度を形成するため、また、
使用時の雰囲気に対する耐食性を高めるために、目的、
用途により添加される。添加する場合には、一般的にMo
単独添加とするが、目的、用途によりMo、Ｗ複合添加あ
るいはＷ単独添加が施されるものである。析出硬化の最
高硬度については、Moが有利であるが、軟化抵抗につい
ては、Ｗが有利となる。本用途の場合、多量の添加は必
要なく、多すぎると被切削性の低下をまねくので、1/2W
＋Moで0.70％以下とし、低すぎると上記添加の効果が得
られないので1/2W＋Moで0.10％以上とする。
Cuは本発明鋼の焼もどし（時効）処理において、Cu−
Fe固溶体の微細析出による析出（時効）硬化をもたら
し、塊状上部ベイナイト基地とあいまって本発明鋼の極
めて優れた被切削性を形成させるための、また所要の硬
さを得るための最も重要な添加元素の一つであり、また
優れた耐食性をもたらすものである。多すぎると熱間加
工性を低下させ、また、ベイナイトを微細化させ、かえ
って被切削性を低下させるので2.50％以下とし、低すぎ
ると上記添加の効果が得られないので1.80％以下とす
る。
Alはベイナイト変態温度を高めて望ましい塊状上部ベ
イナイトを得やすくし、焼もどし（時効）処理におい
て、Ni−Al金属間化合物の微細析出による析出（時効）
硬化をもたらし、塊状上部ベイナイト基地、Cu−Fe固溶
体の析出とあいまって本発明鋼の特徴であるHRC43ない
しそれ以上の高い硬さレベルでの優れた被切削性を形成
させるための極めて重要な添加元素であり、含有量を高
めとするものである。
また、Alの含有は窒化時の窒化硬さを上昇させる効果
をもたらす。多すぎるとアルミナ系介在物の生成傾向が
大きくなり、製造性を低下上させ、また鏡面仕上性や耐
食性を低下させ、さらに延性の過度の低下をまねくので
1.50％以下とし、低すぎると上記添加の効果が得られな
いので0.85％以上とする。
ＳとMnとの間にMnS系介在物を形成し、本願発明鋼の
快削性や研磨仕上性を高めるための不可欠の重要元素で
ある。
本発明鋼の特徴である高い硬さ域での優れた被切削性
の保持はNi−Al金属間化合物、Cu−Fe固溶体の多量に析
出分布した低Ｃのベイナイト基地と、基地に分布する硫
化系介在物の効果によるもので、優れた研磨仕上性にも
寄与するものである。Ｓは多すぎると粗大な硫化物を形
成して靭性を害し、また孔食の発生や鏡面研磨時に過度
のピットの発生をまねくので0.16％以下とし、低すぎる
と上記添加の効果が得られないので0.05％以上とする。
その他Ca、Ce、Zrなどの添加による硫化物の微細化、
均一分散化やSe、Te等快削性付与元素の添加も被切削性
の向上に有効である。
〔発明の効果〕
以上に詳述するように、本発明鋼はHRC43ないしこれ
を越える高い硬さでも、極めて優れた被切削性を備え、
また研磨仕上性が特に優れており、また適度の鏡面仕上
性、優れた耐放電硬化性、シボ加工性を備え、高い強
度、耐摩耗性とあいまって長寿命をもたらすプラスチッ
ク成形プリハードン金型用鋼を提供するものである。DETAILED DESCRIPTION OF THE INVENTION [Industrial Application Field] The present invention is characterized by having an extremely selected machinability even with H R C43 or higher hardness, and has excellent polishing finish. It relates to a new pre-hardened type steel for plastic molding dies. [Prior art] As high-grade plastic molding die steel, (1) good mirror finish, small tendency to generate pinholes and other fine pits, (2) good grain workability, (3) corrosion resistance , Good rust resistance, (4) good strength, wear resistance and toughness, and (5) good machinability. However, in recent years, it has been strongly suggested that the shortening of the hard metal production delivery time in conjunction with the increase in hardness is a particularly important customer requirement. only the method of improve Te was difficult to retain good machinability in H R C43 or higher hardness exceeding this. [Problems to be solved the problems] The present invention has superior machinability at high hardness exceeding H R C43 to this, and with a combined excellent polished finish with high hardness alloys The purpose is to provide. [Means for Solving the Invention] That is, the steel of the present invention has low C-medium to low Mn-Ni-Mo (W).
-High Cu-High Al-S based alloy, which forms a uniform upper bainite structure by quenching.
High-temperature tempering of over ℃ causes low-C bainite
-Precipitates Fe solid solution, Ni-Al intermetallic compound, and Mo (W) carbide, imparts high strength by aging (precipitation) hardening, causes moderate embrittlement, and has extremely good machinability on the base itself. with conferring, together with the distribution of sulfide to impart machinability improving, it holds the excellent polishing finish properties with obtaining excellent machinability in H R C43 or high hardness exceeding this is there. Also, Cr, Mo,
Excellent corrosion resistance and rust resistance are obtained by the inclusion of W, Cu, and Ni, and hardening due to electric discharge machining is small. In this respect, finishing is easy. The steel of the present invention is supplied in a pre-hardened state having a hardness of H R C37 or more (generally tempered at 400 ° C. or higher after quenching), and is used after being subjected to engraving → polishing finish as it is. it is to hold the excellent machinability even R C43 or more. Therefore, without the need for heat treatment by the user, the combination of the highest degree of good machinability, high hardness and a homogeneous base provides extremely excellent polishing finish, and there is a need for concerns about sagging and wear. This is a new plastic molding die steel that can provide a long life without the need. EXAMPLES The present invention will be described below based on examples. Table 1 shows the chemical compositions of Examples of the present invention and Comparative Steels. Comparative steel K is a free-cutting steel, but is a mold steel characterized by being particularly excellent in toughness. Comparative steel L is 0.77%
Although it contains Al and is more excellent in machinability than that of comparative steel K and has appropriate toughness, machinability is inferior to that of the high Al-based steel of the present invention. Despite heat treated H R C44 of the present invention steels in Table 2 shows the machinability index and cutting surfaces maximum Roughness ratio relative to the SCM440 (H R C37.5) in the case of cutting with an end mill. The present invention steel, SCM even at high hardness levels before and after H R C44
440 (H R C37.5) and machinability is significantly better than, also cutting surface Roughness also remarkably fine, show that the effect is larger steps reduce the subsequent polishing. Table 3 shows the mirror finish (pit resistance) of the steel of the present invention in comparison with comparative steels L and M. Article ShoIri in H R C44 with 50mm square, after tempering treatment, grinding → paper → performs mirror finish in the manner of a diamond compound polishing, obtained by counting the fine pits generated number using the 10x magnifier is there. The steel of the present invention has a high hardness and has a lower tendency to generate pits than the comparative steels L and M. Table 4 shows the required polishing finish time after cutting of the steel of the present invention in comparison with that of the conventional steel. The sample is 50mm x 50mm.After the heat treatment, after cutting by end mill, mirror finish is performed by the method of grinding stone → paper → diamond compound polishing. It is shown. The steel of the present invention has a high hardness, does not produce deep polishing marks, and, together with the dispersion of sulfides, smoothly removes chips during polishing and exhibits excellent polishing finish. Next, the reasons for limiting the components of the steel of the present invention will be described. C keeps the hardened structure of the steel of the present invention in a massive upper bainite structure with good machinability, and prevents precipitation hardening due to precipitation of Cu-Fe solid solution, Ni-Al intermetallic compound and Mo, W carbide in tempering. It is a basic additive element to provide a substrate to provide. If the content is too large, the matrix becomes a martensite structure to reduce machinability, and excessive carbides are formed to reduce machinability. In addition, it deteriorates the electric discharge machining property, reduces the mirror surface finish, further enhances the electric discharge hardening property, and increases the number of polishing processes after the electric discharge machining, so that it is 0.17% or less. Since tempering (aging) hardness cannot be obtained, the content is set to 0.08% or more in relation to Al and other alloy compositions. Mn is added to enhance the bainite hardenability of the steel of the present invention, to suppress the formation of ferrite, and to provide appropriate quenching and tempering (aging) hardness. If it is too large, the bainite transformation temperature is lowered, the bainite structure is excessively refined, and the machinability is increased by lowering the viscosity of the matrix.
If it is too low, the effect of the above-mentioned addition cannot be obtained, so it is made 0.50% or more. Si is added depending on the purpose and application in order to increase the corrosion resistance against the atmosphere during use. If the content is too large, ferrite is formed and the machinability is reduced. Ni enhances the bainite hardenability of the steel of the present invention, suppresses the formation of ferrite, and precipitates a Ni-Al intermetallic compound during tempering (aging) to obtain the high hardness characteristic of the steel of the present invention. At the same time, it is added in order to appropriately reduce ductility and obtain an improvement in machinability. If it is too large, it lowers the bainite transformation temperature, excessively refines the bainite structure, and increases the viscosity of the matrix to reduce machinability, so 3.50%
If the amount is too low, the effect of the above addition cannot be obtained.
2.50% or more. Cr is added depending on the purpose and application in order to increase the corrosion resistance and hardness of the steel of the present invention during nitriding, and to suppress rusting during polishing or storage of a mold. If the content is too large, the bainite structure is refined, and it becomes difficult to maintain the characteristics of the steel of the present invention aimed at particularly high machinability.
50% or less. W and Mo precipitate fine carbides in the high-temperature tempering (aging) treatment of the steel of the present invention exceeding 500 ° C. to bring about precipitation (aging) hardening and to form the strength of the steel of the present invention.
The purpose, in order to increase the corrosion resistance to the atmosphere during use,
It is added depending on the application. When added, generally Mo
Mo is added alone, but Mo or W is added in combination or W is added alone depending on the purpose and application. Mo is advantageous for the maximum hardness of the precipitation hardening, but W is advantageous for the softening resistance. In the case of this application, a large amount of addition is not necessary.
+ Mo is set to 0.70% or less, and if it is too low, the effect of the above addition is not obtained. Therefore, 1 / 2W + Mo is set to 0.10% or more. Cu is used in the tempering (aging) treatment of the steel of the present invention.
The most important addition to bring about the precipitation (aging) hardening due to the fine precipitation of Fe solid solution, to form the excellent machinability of the steel of the present invention in combination with the massive upper bainite matrix, and to obtain the required hardness It is one of the elements and provides excellent corrosion resistance. If the amount is too large, the hot workability is reduced, and the bainite is refined, so that the machinability is rather reduced. Thus, the content is set to 2.50% or less. Al raises the bainite transformation temperature to make it easier to obtain the desired massive upper bainite, and in the tempering (aging) treatment, precipitation by fine precipitation of the Ni-Al intermetallic compound (aging)
It resulted in cure, crucial for the formation of excellent machinability in massive upper bainite base, which is a feature of the combination present invention steels and the precipitation of Cu-Fe solid solution H R C43 or more higher hardness levels It is an additional element that increases the content. Further, the inclusion of Al has an effect of increasing the nitriding hardness during nitriding. If the content is too large, the tendency to form alumina-based inclusions increases, lowering the manufacturability, lowering the mirror finish and corrosion resistance, and further causing excessive reduction in ductility.
If it is too low, the effect of the above-mentioned addition cannot be obtained, so it is made 0.85% or more. An MnS-based inclusion is formed between S and Mn, and is an indispensable important element for improving the free-cutting property and the polishing finish of the steel of the present invention. The excellent machinability retention in the high hardness region, which is a feature of the steel of the present invention, is due to the Ni-Al intermetallic compound, a low C bainite matrix in which a large amount of Cu-Fe solid solution precipitates and distributes, and the sulfide This is due to the effect of system inclusions and contributes to excellent polishing finish. If S is too large, coarse sulfides are formed to impair toughness, and pitting is generated and excessive pits are generated during mirror polishing. Therefore, the content of S is set to 0.16% or less. Therefore, it should be 0.05% or more. Refinement of sulfide by addition of Ca, Ce, Zr, etc.
Uniform dispersion and addition of free-machining elements such as Se and Te are also effective in improving machinability. As detailed above [Effect of the Invention] In the present invention steels H R C43 or higher hardness exceeding this, with a very good machinability,
In addition, it has excellent polishing finish, and has moderate mirror finish, excellent discharge hardening resistance, and excellent crimp workability. Is provided.
───────────────────────────────────────────────────── フロントページの続き (56)参考文献 特開 昭55−28384（ＪＰ，Ａ) 特開 昭60−174854（ＪＰ，Ａ) 特開 昭61−163248（ＪＰ，Ａ) 特公 昭55−29148（ＪＰ，Ｂ２) ────────────────────────────────────────────────── ─── Continuation of front page (56) References JP-A-55-28384 (JP, A) JP-A-60-174854 (JP, A) JP-A-61-163248 (JP, A) Tokiko 55-29148 (JP, B2)
Claims (1)
％、Ni 2.50〜3.50％、Al 0.85％〜1.50％、Cu 1.80〜
2.50％、S 0.05〜0.16％、残部Feおよび通常の不純物よ
りなることを特徴とするプラスチック成形プリハードン
金型用鋼。 ２．C 0.08〜0.17％、Si 0.60％以下、Mn 0.50〜1.20
％、Ni 2.50〜3.50％、Mo、Ｗ単独または複合で1/2W＋M
o 0.10〜0.70％、Al 0.85〜1.50％、Cu 1.80〜2.50％、
S 0.05〜0.16％、残部Feおよび通常の不純物よりなるこ
とを特徴とするプラスチック成形プリハードン金型用
鋼。 ３．C 0.08〜0.17％、Si 0.60％以下、Mn 0.50〜1.20
％、Ni 2.50〜3.50％、Cr 0.50％以下、Al 0.85〜1.50
％、Cu 1.80〜2.50％、S 0.05〜0.16％、残部Feおよび
通常の不純物よりなることを特徴とするプラスチック成
形プリハードン金型用鋼。 ４．C 0.08〜0.17％、Si 0.60％以下、Mn 0.50〜1.20
％、Ni 2.50〜3.50％、Cr 0.50％以下、Mo、Ｗ単独また
は複合で1/2W＋Mo 0.10〜0.70％、Al 0.85〜1.50％、Cu
1.80〜2.50％、S 0.05〜0.16％、残部Feおよび通常の
不純物よりなることを特徴とするプラスチック成形プリ
ハードン金型用鋼。(57) [Claims] C 0.08 to 0.17%, Si 0.60% or less, Mn 0.50 to 1.20
%, Ni 2.50 ~ 3.50%, Al 0.85% ~ 1.50%, Cu 1.80 ~
Pre-hardened steel for plastic molding, characterized by being composed of 2.50%, S 0.05-0.16%, balance Fe and usual impurities. 2. C 0.08 to 0.17%, Si 0.60% or less, Mn 0.50 to 1.20
%, Ni 2.50-3.50%, Mo, W alone or 1 / 2W + M in combination
o 0.10 ~ 0.70%, Al 0.85 ~ 1.50%, Cu 1.80 ~ 2.50%,
Pre-hardened plastic mold steel, characterized by comprising 0.05-0.16% S, balance Fe and usual impurities. 3. C 0.08 to 0.17%, Si 0.60% or less, Mn 0.50 to 1.20
%, Ni 2.50 to 3.50%, Cr 0.50% or less, Al 0.85 to 1.50
%, Cu 1.80 ~ 2.50%, S 0.05 ~ 0.16%, balance Fe and usual impurities, plastic pre-hardened mold steel. 4. C 0.08 to 0.17%, Si 0.60% or less, Mn 0.50 to 1.20
%, Ni 2.50-3.50%, Cr 0.50% or less, Mo, W alone or in combination, 1 / 2W + Mo 0.10-0.70%, Al 0.85-1.50%, Cu
Pre-hardened plastic mold steel characterized by comprising 1.80-2.50%, S 0.05-0.16%, balance Fe and usual impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62015840A JP2746878B2 (en) | 1987-01-26 | 1987-01-26 | Plastic molding pre-hardened steel for mold |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62015840A JP2746878B2 (en) | 1987-01-26 | 1987-01-26 | Plastic molding pre-hardened steel for mold |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS63183158A JPS63183158A (en) | 1988-07-28 |
| JP2746878B2 true JP2746878B2 (en) | 1998-05-06 |
Family
ID=11900028
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP62015840A Expired - Lifetime JP2746878B2 (en) | 1987-01-26 | 1987-01-26 | Plastic molding pre-hardened steel for mold |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2746878B2 (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH02197548A (en) * | 1989-01-25 | 1990-08-06 | Kobe Steel Ltd | Preharden steel having excellent specular finishing properties and machinability |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5937738B2 (en) * | 1979-04-16 | 1984-09-11 | 大同特殊鋼株式会社 | Age-hardening free-cutting steel for plastic molds |
-
1987
- 1987-01-26 JP JP62015840A patent/JP2746878B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPS63183158A (en) | 1988-07-28 |
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| EXPY | Cancellation because of completion of term |