JPS63183158A - Steel for prehardening metal mold for plastic molding - Google Patents
Steel for prehardening metal mold for plastic moldingInfo
- Publication number
- JPS63183158A JPS63183158A JP1584087A JP1584087A JPS63183158A JP S63183158 A JPS63183158 A JP S63183158A JP 1584087 A JP1584087 A JP 1584087A JP 1584087 A JP1584087 A JP 1584087A JP S63183158 A JPS63183158 A JP S63183158A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- machinability
- hardness
- present
- low
- 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
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 44
- 239000010959 steel Substances 0.000 title claims abstract description 44
- 238000010137 moulding (plastic) Methods 0.000 title claims description 5
- 239000002184 metal Substances 0.000 title abstract 2
- 229910052751 metal Inorganic materials 0.000 title abstract 2
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 6
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 3
- 239000012535 impurity Substances 0.000 claims 4
- 239000000203 mixture Substances 0.000 abstract description 5
- 238000005496 tempering Methods 0.000 abstract description 4
- 229910052802 copper Inorganic materials 0.000 abstract description 3
- 229910052804 chromium Inorganic materials 0.000 abstract description 2
- 229910052748 manganese Inorganic materials 0.000 abstract 1
- 235000019589 hardness Nutrition 0.000 description 21
- 238000005498 polishing Methods 0.000 description 18
- 229910001563 bainite Inorganic materials 0.000 description 15
- 230000000694 effects Effects 0.000 description 9
- 238000005260 corrosion Methods 0.000 description 8
- 230000007797 corrosion Effects 0.000 description 8
- 238000001556 precipitation Methods 0.000 description 8
- 230000032683 aging Effects 0.000 description 7
- 230000000052 comparative effect Effects 0.000 description 6
- 229910000765 intermetallic Inorganic materials 0.000 description 6
- 229910003310 Ni-Al Inorganic materials 0.000 description 5
- 150000001247 metal acetylides Chemical class 0.000 description 4
- 238000000034 method Methods 0.000 description 4
- 229910000859 α-Fe Inorganic materials 0.000 description 4
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 3
- 239000000654 additive Substances 0.000 description 3
- 230000000996 additive effect Effects 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- 238000005121 nitriding Methods 0.000 description 3
- 238000010791 quenching Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 230000009466 transformation Effects 0.000 description 3
- 229910002549 Fe–Cu Inorganic materials 0.000 description 2
- 238000000137 annealing Methods 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 229910003460 diamond Inorganic materials 0.000 description 2
- 239000010432 diamond Substances 0.000 description 2
- 238000009760 electrical discharge machining Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 2
- 238000003754 machining Methods 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000004881 precipitation hardening Methods 0.000 description 2
- 150000003568 thioethers Chemical class 0.000 description 2
- 229910052684 Cerium Inorganic materials 0.000 description 1
- 229910000915 Free machining steel Inorganic materials 0.000 description 1
- 229910000760 Hardened steel Inorganic materials 0.000 description 1
- 229910018062 Ni-M Inorganic materials 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 229910052791 calcium Inorganic materials 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000011521 glass Substances 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 238000004904 shortening Methods 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Landscapes
- Moulds For Moulding Plastics Or The Like (AREA)
Abstract
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
めて優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。[Detailed Description of the Invention] [Industrial Application Field] The present invention is a new pre-hardened steel which is characterized by having extremely excellent machinability even at a high hardness of HRC43 or higher, and which also has excellent polishing finish properties. This relates to steel for type plastic molds.
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。As a steel for high-grade plastic molds, it should (1) have a good mirror finish and have a small tendency to form pinholes and other fine pits, and (2) have good texturability.
（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。(3) good corrosion resistance and rust resistance; (4) good strength, wear resistance, and toughness; and (5) good machinability.
しかし、近年高硬度化と併せて型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。However, in recent years, shortening mold manufacturing lead times has been strongly raised as a particularly important customer demand in conjunction with increasing hardness, but it has not been possible to simply add free-machining elements such as S to improve machinability as in the past. It has been difficult to maintain excellent machinability at hardnesses of HRC43 or higher using only methods that aim for improvement.
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。The object of the present invention is to provide an alloy that has a high hardness of HRC43 or higher and has excellent machinability, and combined with the high hardness, has an extremely excellent polishing finish.
すなわち、本発明鋼は低Ｃ−中〜低Ｍｎ−Ｎｉ−Ｍ。 That is, the steel of the present invention has low C-medium to low Mn-Ni-M.
（Ｗ）−高Ｃｕ−高Ａｔ−８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Ｆｅ＝Ｃｕ、Ｎｉ−Ａｌ金属間化合物、Ｍ
ｏ （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、Ｈ
ＲＣ４３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。It is an alloy whose basic components are (W)-high Cu-high At-8, and it produces a uniform upper bainite structure by quenching.
Furthermore, by high-temperature annealing at a temperature of 500°C or higher, Fe=Cu, Ni-Al intermetallic compounds, M
o (W) Precipitates carbides, imparts high strength through aging (precipitation) hardening, and causes moderate embrittlement,
In addition to imparting extremely good machinability to the base itself,
Coupled with the distribution of sulfide to impart free machinability, H
It provides extremely excellent machinability at high hardness of RC43 or higher and maintains excellent polishing finish.
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。In addition, the inclusion of Cr, Mo, W, Cu, and Ni provides excellent corrosion resistance and rust resistance, and furthermore, hardening due to electrical discharge machining is small, and finishing processing is easy in this respect as well.
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。The steel of the present invention is supplied in a pre-hardened state (generally tempered at 400°C or higher after quenching) with a hardness of HRC 37 or higher, and is used as it is by die-carving and polishing. Even with the above, excellent machinability is maintained.
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。Therefore, no heat treatment is required by the user, and the combination of the highest degree of good machinability, high hardness and homogeneous base,
This is a new steel for plastic molds that provides an extremely excellent polishing finish, eliminates concerns about settling or wear, and provides a long service life.
以下本発明を実施例に基づき説明する。 The present invention will be explained below based on examples.
第１表に本発明鋼の実施例と比較鋼の化学成分を示す。Table 1 shows the chemical compositions of Examples of the steels of the present invention and comparative steels.
比較ｍＫ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ＭＬは０．７７％の
Ａｌを含有し、被切削性は比較鋼にのそれよりも優れて
おり、適度の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。Although comparative mK is a free-cutting steel, it is a mold steel characterized by particularly excellent toughness. Comparative ML contains 0.77% Al, has better machinability than the comparative steel, and has moderate toughness, but is less susceptible to machining than the high-Al steel of the present invention. Machinability is poor.
第 １ 表
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）を基本とした被切削性指数および切削面最大アラサ
比を示す。Table 1 Table 2 shows SCM440 (HRC37,
The machinability index and maximum roughness ratio of the cut surface based on 5) are shown.
第 ２ 表
本発明鋼は、ＨＲＣ４４前後の高い硬さ水準においても
Ｓ ＣＭ 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。Table 2 The steel of the present invention has much better machinability than S CM 440 (HRC37,5) even at a high hardness level of around HRC44, and the roughness of the cut surface is much finer, making it easier to process after polishing. This shows that it is highly effective in reducing man-hours.
第３表は、本願発明鋼の鏡面仕上性（耐ピット性）を比
較＠Ｌ、Ｍと対比したものである。Table 3 compares the mirror finish (pit resistance) of the invention steel with L and M.
試料は５０ｎｎ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。The samples are 50 nn square HRC44 hardened and tempered, polished to a mirror finish using a grinder → paper → diamond compound polishing method, and the number of minute pits generated was counted using a 10x magnifying glass.
第３表
本発明鋼は硬さが高く、比較鋼り、Ｍに対比してピット
発生の傾向が小さい。Table 3 The steels of the present invention have high hardness and have a smaller tendency to form pits than the comparative steel M.
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。Table 4 shows the time required for polishing after cutting of the steel of the present invention in comparison with that of conventional steel.
試料は５０＋＋ｎＸ５０ｍｍ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。The sample was 50++n x 50mm, and after heat treatment, it was cut with an end mill, and then polished to a mirror finish using a grindstone → paper → diamond compound polishing method. The time required to complete the finish was expressed as an index, with that of comparative steel M set as 100. It is something.
第４表 本願発明鋼は硬さが高く、深い研磨痕を生じず。Table 4 The steel of the present invention has high hardness and does not produce deep polishing marks.
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。In addition, together with the dispersion of sulfides, the removal of chips during polishing is performed smoothly, resulting in excellent polishing finish.
次に本発明鋼の成分限定理由について述べる。Next, the reasons for limiting the composition of the steel of the present invention will be described.
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−Ｆ
ｅ、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。C maintains the quenched structure of the steel of the present invention into a blocky upper bainite structure with good machinability, and C maintains the quenched structure of the steel of the present invention into a blocky upper bainite structure with good machinability.
E, Ni-Al intermetallic compound and Mo, is a basic additive element for providing a substrate for precipitation hardening based on the precipitation of W carbides. If it is too large, the matrix becomes martensitic, reducing machinability, and excessive carbides are formed, reducing machinability.
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く時効）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。In addition, it deteriorates electrical discharge machinability, reduces mirror finish properties, increases electrical discharge hardenability, and increases the number of polishing steps after electrical discharge machining, so it should be set at 0.17% or less. If it is too low, it may lead to ferrite precipitation, and Since sufficient tempering and aging hardness cannot be obtained, the relationship with the alloy composition of Al and others is 0.
08% or more.
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、焼もどしく時効）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。Mn is added to improve the bainite hardenability of the steel of the present invention, to suppress the formation of ferrite, and to provide appropriate quenching, tempering, and aging hardness. If it is too large, it will lower the bainite transformation temperature, make the bainite structure excessively fine, and increase the viscosity of the base, reducing machinability.
．． The content should be 20% or less, and if it is too low, the effect of the above addition cannot be obtained, so the content should be 0.50% or more.
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。Si is added depending on the purpose and use in order to improve corrosion resistance against the atmosphere during use. 0.60% as too much will lead to the formation of ferrite and reduce machinability.
The following shall apply.
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、焼もどしく時効）時、Ｎｉ−Ａｌ
金属間化合物を析出させ１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力９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。Ni improves the bainitic hardenability of the steel of the present invention, suppresses the formation of ferrite, and when tempered and aged), Ni-Al
A loading force of 9 is applied to precipitate intermetallic compounds to obtain the high hardness characteristic of the steel of the present invention, moderately reduce ductility, and improve machinability. If it is too high, it will lower the bainite transformation temperature, make the bainite structure excessively fine, and increase the viscosity of the base, reducing machinability, so it should be 3.50% or less, and if it is too low, the effect of the above addition will not be achieved. Therefore, it should be set at 2.50% or more.
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。Cr is added depending on the purpose and use in order to increase the corrosion resistance of the steel of the present invention and its hardness during nitriding, and to suppress rusting during polishing or storage of molds.
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。If it is too large, the bainite structure becomes fine and it becomes difficult to maintain the characteristics of the steel of the present invention, which aims at particularly high machinability, so the content is set to 0.50% or less.
Ｗ、Ｍｏは本発明鋼の５００℃を越える高温節もどしく
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６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。W and Mo precipitate fine carbides during the high-temperature aging process of the steel of the present invention at temperatures exceeding 500°C.
It is added depending on the purpose and use, in order to harden the steel of the present invention and increase its corrosion resistance against the atmosphere during use. When added, Mo is generally added alone, but a combination of Mo and W or W alone may be added depending on the purpose and use. Regarding the maximum hardness of precipitation hardening, Mo is advantageous, but regarding softening resistance, W is advantageous in the case of 6 applications, it is not necessary to add a large amount, and too much will lead to a decrease in machinability. 1/2W+Mo should be 0.70% or less. If it is too low, the effect of the above addition cannot be obtained, so 1/2W+Mo should be 0.70% or less.
10% or more.
Ｃｕは本発明鋼の焼もどしく時効）処理において。Cu is used in the tempering and aging treatment of the steel of the present invention.
Ｆｅ−Ｃｕ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％以上とする。Precipitation by fine precipitation of Fe-Cu intermetallic compound (aging)
In order to bring about hardening and form the extremely excellent machinability of the steel of the present invention in combination with the massive upper bainite base,
It is also one of the most important additive elements for obtaining the required hardness and provides excellent corrosion resistance. If it is too high, hot workability will be reduced, and bainite will become finer, which will actually reduce machinability, so 2.50%.
If the content is too low, the effect of the above addition cannot be obtained, so the content should be 1.80% or more.
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、焼もどしく時効）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−Ｆ
ｅ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
を高めどするものである。Al increases the bainite transformation temperature to facilitate obtaining the desired massive upper bainite, and in the annealing and aging treatment, it leads to precipitation (age) hardening due to fine precipitation of Ni-Al intermetallic compounds, forming a massive upper bainite matrix, Cu- F
Combined with the precipitation of e, HRC43 is a characteristic of the steel of the present invention.
It is an extremely important additive element for achieving excellent machinability at or above a high hardness level, and its content should be increased.
また、ＡＩ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。In addition, the content of AI has the effect of increasing the nitriding hardness during nitriding, and if it is too large, the tendency to generate alumina-based inclusions increases, reducing manufacturability, as well as reducing mirror finish and corrosion resistance. 1 because it causes an excessive decrease in ductility.
．． The content should be 50% or less, and if it is too low, the effect of the above addition cannot be obtained, so the content should be 0.85% or more.
Ｓは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。S forms MnS-based inclusions with Mn, and is an essential element for improving the free machinability and polishing finish of the steel of the present invention.
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、Ｆｅ−Ｃｕ金属間化合物の多量に析
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。The excellent machinability in the high hardness range, which is a feature of the steel of the present invention, is due to the low C bainite base with a large amount of Ni-Al and Fe-Cu intermetallic compounds precipitated and distributed, and the sulfide base distributed in the base. This is due to the effect of inclusions and also contributes to excellent polishing finish. If S is too large, it will form coarse sulfides, impairing toughness, and cause pitting corrosion and excessive pitting during mirror polishing, so it should be 0.16% or less, and if it is too low, the effect of the above addition will not be achieved. Therefore, it should be set at 0.05% or more.
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Ｓｓ、Ｔｓ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。In addition, making the sulfide finer and more uniformly dispersed by adding Ca, Ce, Zr, etc., and adding free machinability imparting elements such as Ss, Ts, etc. are also effective in improving machinability.
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。As detailed above, the steel of the present invention has extremely excellent machinability even with a high hardness of HRC 43 or higher, and has particularly excellent polishing finish.
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。The present invention also provides a steel for pre-hardened molds for plastic molding, which has a suitable mirror finish, excellent electrical discharge hardening resistance, and texturing properties, and which, in combination with high strength and wear resistance, provides a long life.
Claims (1)
ｎ０．５０〜１．２０％、Ｎｉ２．５０〜３．５０％、
Ａｌ０．８５〜１．５０％、Ｃｕ１．８０〜２．５０％
、Ｓ０．０５〜０．１６％、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 Ｃ０．０８〜０．１７％、Ｓｉ０．６０％以下、
Ｍｎ０．５０〜１．２０％、Ｎｉ２．５０〜３．５０％
、Ｍｏ、Ｗ単独または複合で１／２Ｗ＋Ｍｏ０．１０〜
０．７０％、Ａｌ０．８５〜１．５０％、Ｃｕ１．８０
〜２．５０％、Ｓ０．０５〜０．１６％、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 Ｃ０．０８〜０．１７％、Ｓｉ０．６０％以下、Ｍ
ｎ０．５０〜１．２０％、Ｎｉ２．５０〜３．５０％、
Ｃｒ０．５０％以下、Ａｌ０．８５〜１．５０％、Ｃｕ
１．８０〜２．５０％、Ｓ０．０５〜０．１６％、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 Ｃ０．０８〜０．１７％、Ｓｉ０．６０％以下、Ｍ
ｎ０．５０〜１．２０％、Ｎｉ２．５０〜３．５０％、
Ｃｒ０．５０％以下、Ｍｏ、Ｗ単独または複合で１／２
Ｗ＋Ｍｏ０．１０〜０．７０％、Ａｌ０．８５〜１．５
０％、Ｃｕ１．８０〜２．５０％、Ｓ０．０５〜０．１
６％、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。[Claims] 1 C 0.08 to 0.17%, Si 0.60% or less, M
n0.50-1.20%, Ni2.50-3.50%,
Al0.85-1.50%, Cu1.80-2.50%
, S0.05-0.16%, balance Fe and normal impurities. 2 C0.08-0.17%, Si0.60% or less,
Mn 0.50-1.20%, Ni 2.50-3.50%
, Mo, W alone or in combination 1/2W+Mo0.10~
0.70%, Al0.85-1.50%, Cu1.80
-2.50%, S0.05-0.16%, balance Fe and normal impurities. Steel for plastic molding pre-hardened molds. 3 C0.08-0.17%, Si0.60% or less, M
n0.50-1.20%, Ni2.50-3.50%,
Cr0.50% or less, Al0.85-1.50%, Cu
A steel for pre-hardened molds for plastic molding, characterized in that it comprises 1.80-2.50% S, 0.05-0.16% S, and the balance Fe and normal impurities. 4 C0.08-0.17%, Si0.60% or less, M
n0.50-1.20%, Ni2.50-3.50%,
Cr0.50% or less, Mo, W alone or in combination 1/2
W+Mo0.10-0.70%, Al0.85-1.5
0%, Cu1.80-2.50%, S0.05-0.1
6%, the balance being Fe and normal impurities. Steel for plastic molding pre-hardened molds.
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 true JPS63183158A (en) | 1988-07-28 |
| JP2746878B2 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) |
Cited By (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 |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5528384A (en) * | 1979-04-16 | 1980-02-28 | Daido Steel Co Ltd | Steel for age hardening plastic die |
-
1987
- 1987-01-26 JP JP62015840A patent/JP2746878B2/en not_active Expired - Lifetime
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5528384A (en) * | 1979-04-16 | 1980-02-28 | Daido Steel Co Ltd | Steel for age hardening plastic die |
Cited By (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 |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2746878B2 (en) | 1998-05-06 |
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