JP2655840B2 - Plastic forming pre-hardened steel for mold - Google Patents
Plastic forming pre-hardened steel for moldInfo
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- JP2655840B2 JP2655840B2 JP62015841A JP1584187A JP2655840B2 JP 2655840 B2 JP2655840 B2 JP 2655840B2 JP 62015841 A JP62015841 A JP 62015841A JP 1584187 A JP1584187 A JP 1584187A JP 2655840 B2 JP2655840 B2 JP 2655840B2
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- machinability
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Description
【発明の詳細な説明】 〔産業上の利用分野〕 本発明は極めて優れた被切削性、研磨仕上性を有する
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 relates to a new prehardened type steel for plastic molding dies having extremely excellent machinability and polishing finish.
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
トの発生しないこと、 （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、耐摩耗性が良く、適度の靭性を備えている
こと、 （５）被切削性が良いこと、 などが要求される。As high-grade plastic molding die steel, (1) good mirror finish and no pinholes or other fine pits are generated; (2) good crimp workability; and (3) corrosion resistance and rust resistance. Good properties, (4) good strength and wear resistance and moderate toughness, and (5) good machinability are required.
しかし、近年型の製作期間の短縮やプラスチック成形
肌の良好なことが特に重要な顧客要求として提起され、
高い硬さでの優れた被切削性（工具寿命、切削肌）と鏡
面仕上性を兼備した型用鋼の開発が課題となった。However, in recent years, shortening of mold production time and good plastic molding surface have been raised as particularly important customer requirements,
The challenge was to develop mold steel that combines excellent machinability with high hardness (tool life, cutting surface) and mirror finish.
従来型用鋼の切削肌、鏡面仕上性を高めることは、逆
に切削工具の寿命の低下をまねくことにつながり、両者
の特性を兼備させることは容易ではなかった。Increasing the cutting surface and the mirror finish of conventional steel leads to a reduction in the life of the cutting tool, and it is not easy to combine the characteristics of both.
本発明は、上記諸要求性質を同時に満たす合金の提供
を目的とするものである。An object of the present invention is to provide an alloy that satisfies the above-mentioned various properties at the same time.
すなわち、本発明鋼は低Ｃ−中〜低Mn−Ni−Mo（Ｗ）
−高Cu−高Al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−C
u、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、極めて良好な切削肌と工具寿命を
付与するとともに、高い硬さとあいまって、特に優れた
鏡面仕上性を示すものである。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、また
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。That is, the steel of the present invention has low C-medium to low Mn-Ni-Mo (W).
-An alloy containing a high Cu-high Al system as a basic component, generates a uniform upper bainite structure by quenching, and furthermore, by high-temperature tempering at 500 ° C or higher, reduces Fe-C
u, to precipitate Ni-Al intermetallic compound and Mo (W) carbide,
While giving high strength by aging (precipitation) hardening,
It causes moderate embrittlement, imparts extremely good cutting surface and tool life, and shows particularly excellent mirror finish in combination with high hardness. Also, Cr, Mo, W, Cu,
Excellent corrosion resistance and rust resistance are obtained by the inclusion of Ni, and hardening due to electric discharge machining is small, and finishing 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→研磨加工、さらに高度の鏡面
仕上性やシボ加工処理を施して使用されるものである。The steel of the present invention is supplied in a pre-hardened state with a hardness of H R C37 or higher (generally tempered at 400 ° C or higher after quenching). It is used after processing.
したがって、ユーザーでの熱処理を要せず、極めて良
好な被切削性、高い硬さと均一なマトリックス、本質的
に優れた鋼質の清浄性とがあいまって、極めて優れた研
磨加工性、鏡面仕上やシボ加工性をもたらし、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, without the need for heat treatment by the user, combined with extremely good machinability, high hardness and uniform matrix, and essentially excellent steel cleanliness, extremely excellent polishing workability, mirror finish and This is a new plastic molding die steel that provides grain workability and allows for a long life without worrying about sagging or wear.
以下本発明を実施例に基づき説明する。 Hereinafter, the present invention will be described 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。比較鋼Ｈは最高級の鏡面仕上肌、シボ加工肌が得ら
れ、かつ靭性が特に優れた型用鋼である。比較鋼Ｉはや
やAl量を低めたもので、靭性は良好であるが、被切削性
は本発明鋼よりも低いものである。比較鋼ＪはSCM440で
ある。Table 1 shows the chemical compositions of Examples of the present invention and Comparative Steels. Comparative steel H is a mold steel having the highest quality mirror-finished skin and textured skin, and having particularly excellent toughness. The comparative steel I had a slightly lower Al content and had good toughness, but had lower machinability than the steel of the present invention. Comparative steel J is SCM440.
第２表に本発明鋼のHRC43に熱処理したもののエンド
ミルによる切削の場合のSCM440（HRC35）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。 Despite heat treated H R C43 of the present invention steels in Table 2 shows the machinability index and cutting surfaces maximum Roughness ratio relative to the SCM440 (H R C35) in the case of cutting with an end mill.
本発明鋼は、HRC43前後の高い硬さ水準においてもSCM
440（HRC35.1）よりも比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。 The present invention steel, SCM even at high hardness levels before and after H R C43
440 (H R C35.1) and specific cutting resistance is much better than, also cutting surface Roughness also remarkably fine, show that the effect is larger steps reduce the subsequent polishing.
第３表は、本発明鋼の断面寸法50mmt×150mmw鍛伸材
につき、HRC43前後に焼入焼もどし後、試験片を鍛伸方
向に対し平行（Ｌ）および直角（Ｔ）方向に採取して引
張試験およびシャルピー衝撃試験（2mmμノッチ）を行
なった結果を示す。Table 3, for each cross-sectional dimension 50mmt × 150mmw forged material of the present invention steel, after tempering quenching sintered around H R C43, a test piece in parallel (L) and quadrature (T) direction relative to forging direction taken The results of a tensile test and a Charpy impact test (2 mmμ notch) were shown.
本発明鋼は、比較鋼Ｉに対比して引張試験における伸
び、絞り値およびシャルピー衝撃値は低く、これが切削
加工時の切粉の剪断による削除を極めて容易にし、これ
により切削工具の寿命や切削面のアラサが特に良好で、
比較鋼ＩやＪ（SCM440）に対し被切削面が大きく高めら
れている。 The steel of the present invention has a low elongation, a draw value and a Charpy impact value in a tensile test as compared with the comparative steel I, which makes it very easy to remove chips by shearing during cutting, thereby shortening the life of the cutting tool and cutting life. Arasa on the surface is particularly good,
The surface to be cut is greatly increased compared to comparative steels I and J (SCM440).
一方、伸び、絞りおよびシャルピー衝撃値は低いた
め、複雑形状や薄肉部を有する型として使用する場合に
は、靭性に配慮して、硬さをやや低めにすることが必要
な場合もある。On the other hand, since the elongation, drawing, and Charpy impact values are low, when used as a mold having a complicated shape or a thin portion, it may be necessary to lower the hardness slightly in consideration of toughness.
Al量が本願発明鋼よりも低い比較鋼Ｉの場合、靭性、
延性は良好であるが、極めて優れた被切削性を本位とす
る本発明鋼の被切削性の水準に達しないものである。In the case of the comparative steel I in which the Al content is lower than the steel of the present invention, toughness,
Although the ductility is good, it does not reach the level of machinability of the steel of the present invention, which is based on extremely excellent machinability.
第４表に本発明鋼の塩水雰囲気中における耐発錆試験
の結果を示す。Table 4 shows the results of the rust resistance test of the steel of the present invention in a salt water atmosphere.
試料は25mm×25mmで、ペーパー→バフ鏡面仕上のの
ち、塩水雰囲気中に２時間浸漬した場合の発錆個数を、
Al量が低い比較鋼Ｉのそれを100として指数で示したも
のである。 The sample is 25mm x 25mm, and after paper → buff mirror finish, the number of rusting when immersed in salt water atmosphere for 2 hours,
The index is shown as an index, with that of Comparative Steel I having a low Al content being 100.
本発明鋼は溶解、造塊技術面からの検討により、Alを
含まない比較鋼Ｈには及ばないが、腐食孔発生の原因と
なるAl2O3系非金属介在物の生成を少量に抑えることが
でき、この結果、比較鋼Ｉに準ずる耐発錆個数を維持し
ている。Although the steel of the present invention is not as good as the comparative steel H containing no Al by studying the melting and ingot-making technologies, it suppresses the generation of Al 2 O 3 nonmetallic inclusions that cause corrosion porosity to a small amount. As a result, the number of rust-resistant articles comparable to Comparative Steel I is maintained.
第５表に本発明鋼の切削加工後の研磨仕上の所要時間
を比較鋼と対比して示した。Table 5 shows the required time for the polishing finish after cutting of the steel of the present invention in comparison with the comparative steel.
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
でに要する時間を比較鋼Ｉのそれを100として指数で示
したものである。 The sample is 50mm x 50mm.After heat treatment, after cutting by end mill, mirror finish is performed by the method of grinding stone → paper → diamond compound polishing. It is shown.
本願発明鋼は硬さが高く、深い研磨痕を生じず、研磨
における切粉の除去が円滑に行なわれ、優れた研磨性を
示す。The steel of the present invention has high hardness, does not produce deep polishing marks, smoothly removes chips during polishing, and exhibits excellent polishing properties.
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 components 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−Fe、
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
切削性を減じさせる。C keeps the hardened structure of the steel of the present invention in a massive upper bainite structure with good machinability, and Cu-Fe in tempering,
Based on precipitation of Ni-Al intermetallic compound and Mo, W carbide,
It is a basic additive element for providing a substrate for effecting precipitation hardening. If the content is too large, the matrix becomes martensite-structured to reduce machinability, and excessive carbides are formed to reduce 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（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 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。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 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、延性に適度に低下させ、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。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％未満とする。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.
It shall be less than 50%.
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、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。W and Mo precipitate fine carbides in the high-temperature tempering (aging) treatment of the steel of the present invention exceeding 500 ° C., and cause precipitation (aging) hardening to form the strength of the steel of the present invention.
It is added depending on the purpose and application in order to increase the corrosion resistance to the atmosphere during use. When it is added, Mo is generally added alone, but depending on the purpose and application, Mo and W are added in a combined manner or W is added alone. 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 cannot be obtained. Therefore, 1 / 2W + Mo is set to 0.10% or more.
Cuは本発明鋼の焼もどし（時効）処理において、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。Cu is used in the tempering (aging) treatment of the steel of the present invention.
The precipitation (ageing) hardening due to the fine precipitation of Cu intermetallic compound is combined with the massive upper bainite matrix to form the extremely excellent machinability of the steel of the present invention, and is most important for obtaining the required hardness. One of the additional elements
It also provides excellent corrosion resistance. If it is too large, it reduces the hot workability and also makes bainite finer,
On the contrary, the machinability is reduced, so that the content is set to 2.50% or less.
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とあいまって
本発明鋼の特徴である極めて高い硬さとともに優れた被
切削性を形成させるための重要な添加元素である。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 is an important additive element for bringing about hardening and forming excellent machinability together with the extremely high hardness characteristic of the steel of the present invention in combination with the massive upper bainite matrix.
また、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。Further, an effect of increasing the nitriding hardness during nitriding is brought about. If it is too large, the tendency to form alumina-based inclusions will increase, lowering the manufacturability, lowering the mirror finish and corrosion resistance, and further reducing the ductility. 0.85 because no effect
% Or more.
以上に詳述するように、本発明鋼は基地組成、基地組
織および析出（時効）生成物の適切な組合せにより、HR
C43クラスの硬さでも特に良好な被切削性を保持すると
ともに、研磨仕上工数の低減をもたらし、また優れた鏡
面仕上性、耐孔食性、放電加工性、シボ加工性を有する
プラスチック成形プリハードン（たとえばHRC38〜44）
金型用鋼を提供するものである。As described in detail above, the steels of the present invention can be used with the appropriate combination of matrix composition, matrix structure, and precipitated (aged) product to achieve H R
Even with a C43 class hardness, it retains particularly good machinability, reduces the number of polishing finish man-hours, and also has excellent mirror finish, pitting corrosion resistance, electric discharge machining, and embossing plastic pre-hardened (for example, H R C38-44)
It is intended to provide mold steel.
Claims (4)
〜1.20％、Ni 2.50〜3.50％、Al 0.85〜1.50％、Cu 1.8
0〜2.50％、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。(1) C 0.08 to 0.17%, Si 0.60% or less, Mn 0.50
~ 1.20%, Ni 2.50 ~ 3.50%, Al 0.85 ~ 1.50%, Cu 1.8
Plastic molded pre-hardened mold steel comprising 0 to 2.50%, the balance being Fe and ordinary impurities.
〜1.20％、Ni 2.50〜3.50％、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％、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 to 0.17%, Si 0.60% or less, Mn 0.50
-1.20%, Ni 2.50-3.50%, Mo, W alone or composite 1
/ 2W + Mo 0.10 ~ 0.70%, Al 0.85 ~ 1.50%, Cu 1.80 ~ 2.
Pre-hardened plastic mold steel characterized by the fact that it consists of 50%, balance Fe and usual impurities.
〜1.20％、Ni 2.50〜3.50％、Cr 0.50％未満、Al 0.85
〜1.50％、Cu 1.80〜2.50％、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 to 0.17%, Si 0.60% or less, Mn 0.50
~ 1.20%, Ni 2.50 ~ 3.50%, Cr less than 0.50%, Al 0.85
Pre-hardened mold steel for plastic molding, characterized in that it consists of ~ 1.50%, Cu 1.80 ~ 2.50%, balance Fe and ordinary impurities.
〜1.20％、Ni 2.50〜3.50％、Cr 0.50％未満、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％、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% or less, Mn 0.50
Up to 1.20%, Ni 2.50 to 3.50%, Cr less than 0.50%, Mo, W alone or in combination, 1 / 2W + Mo 0.10 to 0.70%, Al 0.85 to 1.50
%, Cu 1.80-2.50%, balance Fe and usual impurities, plastic molded pre-hardened mold steel.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62015841A JP2655840B2 (en) | 1987-01-26 | 1987-01-26 | Plastic forming pre-hardened steel for mold |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62015841A JP2655840B2 (en) | 1987-01-26 | 1987-01-26 | Plastic forming pre-hardened steel for mold |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS63183153A JPS63183153A (en) | 1988-07-28 |
| JP2655840B2 true JP2655840B2 (en) | 1997-09-24 |
Family
ID=11900054
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP62015841A Expired - Lifetime JP2655840B2 (en) | 1987-01-26 | 1987-01-26 | Plastic forming pre-hardened steel for mold |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2655840B2 (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH02243457A (en) * | 1989-03-17 | 1990-09-27 | Tokyo Electric Co Ltd | Sheet conveying controller |
| JP4853440B2 (en) * | 2007-09-26 | 2012-01-11 | 富士ゼロックス株式会社 | Printing system |
| CN114908301B (en) * | 2019-03-01 | 2023-06-09 | 育材堂（苏州）材料科技有限公司 | Hot work die steel, heat treatment method thereof and hot work die |
Family Cites Families (2)
| 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 |
| JPS61163248A (en) * | 1985-01-09 | 1986-07-23 | Kobe Steel Ltd | Steel for metallic mold for plastic molding |
-
1987
- 1987-01-26 JP JP62015841A patent/JP2655840B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPS63183153A (en) | 1988-07-28 |
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