JPH01104749A - Tool steel for forming light alloy - Google Patents
Tool steel for forming light alloyInfo
- Publication number
- JPH01104749A JPH01104749A JP25872087A JP25872087A JPH01104749A JP H01104749 A JPH01104749 A JP H01104749A JP 25872087 A JP25872087 A JP 25872087A JP 25872087 A JP25872087 A JP 25872087A JP H01104749 A JPH01104749 A JP H01104749A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- hardness
- tool steel
- light alloy
- forming light
- 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
- 229910001234 light alloy Inorganic materials 0.000 title abstract description 7
- 229910001315 Tool steel Inorganic materials 0.000 title abstract description 5
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 229910052742 iron Inorganic materials 0.000 claims description 3
- 229910000831 Steel Inorganic materials 0.000 abstract description 16
- 239000010959 steel Substances 0.000 abstract description 16
- 239000000463 material Substances 0.000 abstract description 14
- 238000000034 method Methods 0.000 abstract description 12
- 238000005121 nitriding Methods 0.000 abstract description 12
- 229910052782 aluminium Inorganic materials 0.000 abstract description 4
- 229910052804 chromium Inorganic materials 0.000 abstract description 4
- 229910052748 manganese Inorganic materials 0.000 abstract description 4
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 4
- 229910052759 nickel Inorganic materials 0.000 abstract description 4
- 238000003754 machining Methods 0.000 abstract description 3
- 239000000203 mixture Substances 0.000 abstract description 3
- 238000004904 shortening Methods 0.000 abstract description 2
- 238000012986 modification Methods 0.000 abstract 1
- 230000004048 modification Effects 0.000 abstract 1
- 238000005496 tempering Methods 0.000 description 7
- 238000001556 precipitation Methods 0.000 description 6
- 238000001125 extrusion Methods 0.000 description 5
- 238000010791 quenching Methods 0.000 description 5
- 230000000171 quenching effect Effects 0.000 description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- 229910001563 bainite Inorganic materials 0.000 description 4
- 229910000765 intermetallic Inorganic materials 0.000 description 4
- 150000004767 nitrides Chemical class 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 230000009466 transformation Effects 0.000 description 3
- BYFGZMCJNACEKR-UHFFFAOYSA-N aluminium(i) oxide Chemical compound [Al]O[Al] BYFGZMCJNACEKR-UHFFFAOYSA-N 0.000 description 2
- 239000003795 chemical substances by application Substances 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- 101100128225 Bacillus subtilis (strain 168) licT gene Proteins 0.000 description 1
- 102220497186 WD repeat domain phosphoinositide-interacting protein 4_N15A_mutation Human genes 0.000 description 1
- 230000005856 abnormality Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000003009 desulfurizing effect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 238000007665 sagging Methods 0.000 description 1
- 239000000523 sample Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
Landscapes
- Mounting, Exchange, And Manufacturing Of Dies (AREA)
- Moulds For Moulding Plastics Or The Like (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は、アルミ合金など軽合金の押し出し成形に用い
るダイス鋼の材質に関するものである。DETAILED DESCRIPTION OF THE INVENTION [Field of Industrial Application] The present invention relates to the material of die steel used for extrusion molding of light alloys such as aluminum alloys.
アルミサツシを代表とする、軽合金の成形は、主に押し
出し成形法が用いられており、このダイスには５ＫＤ６
１鋼に窒化処理を施して使用されてきた。The extrusion method is mainly used to form light alloys, such as aluminum sash, and this die uses 5KD6
1 steel has been nitrided and used.
５ＫＤ６１を押し出しダイスとして用いる場合２つの方
法がある。１つは使用者が焼鈍材を荒加工後、焼入れ焼
もどしを行ない、次に仕上加工の後、窒化処理する方法
である。もう１つは、鋼材メーカで熱処理済みの調質材
を仕上加工し、窒化処理してそのままダイスとして使用
する方法である。最近の押し出し材の形状多様化にとも
ない、ダイス形状の設計変更の頻度も高くなり、このた
めダイス製造に対しても工程短縮が求められている。こ
のような要求に対し、前者のような使用者が加工後熱処
理する工程では、工程短縮は困難であり、また熱処理設
備も必要とすることから、現実的ではない。このため調
質材を仕上加工まで行ない窒化処理後そのまま使用する
後者の方法がとられてきた。この場合、機械加工が可能
であるためには調質材の硬さはできるだけ低い方が望ま
しい。反面ダイス工具としての強度を確保するためには
、高硬度が要求される。これらの相反する要求から、従
来は機械加工性を犠牲にして、１（ＲＣ４０前後の硬さ
で使用されてきた。しかし、表面は窒化処理により高硬
度を有するが内部硬さはＨＲＣ４０前後ではダイス鋼と
して不十分であり、ヘタリが主原因となり、短寿命とな
っていた。このような背景から、ダイス加工の段階では
、被削性をよくするために十分硬さが低く、かつ窒化処
理において内部硬さが、十分に硬化する材質が求められ
ていた。There are two methods when using 5KD61 as an extrusion die. One is a method in which the user roughly processes the annealed material, then quenching and tempering it, then finishing it and then subjecting it to nitriding treatment. The other method is to finish heat-treated tempered material at a steel material manufacturer, nitridize it, and use it as a die as it is. With the recent diversification of shapes of extruded materials, the frequency of changes in the design of die shapes has increased, and therefore there is a need to shorten the process for manufacturing dies. In response to such a request, it is difficult to shorten the process in the former process in which the user performs heat treatment after processing, and heat treatment equipment is also required, which is not realistic. For this reason, the latter method has been adopted, in which the tempered material is subjected to finishing processing and then used as is after nitriding. In this case, it is desirable that the hardness of the tempered material be as low as possible in order to enable machining. On the other hand, high hardness is required to ensure strength as a die tool. Due to these conflicting requirements, conventionally, a hardness of around 1 (RC40) has been used at the expense of machinability.However, although the surface has high hardness due to nitriding, the internal hardness is around HRC40. It was insufficient as a steel, and the main cause was sagging, resulting in a short life.For this reason, at the die processing stage, the hardness was sufficiently low to improve machinability, and the nitriding treatment There was a need for a material with sufficient internal hardness.
本発明は、−二のような要求に対してなされたものであ
り、機械加工が容易でありかつ、窒化処理時において、
十分な内部硬さの得られる材質を提供とするものである
。The present invention has been made in response to the second requirement, and is easy to machine and has the following characteristics:
The material is intended to provide sufficient internal hardness.
本発明は、重量％でＣ０，１２〜０．３％、Ｓｉ１％以
下、Ｍｎ１％以下、Ｎｉ １．５〜４．０％、Ｃｒ００
８〜３．０％、Ｍｏ０．５〜２．０％、／ｊ２０．８〜
２．０％を含み、残部Ｆｅおよび不可避的不純物元素か
らなることを特徴とする軽合金成形用工具鋼である。本
発明の特徴は、窒化処理温度（５２０〜５６０°Ｃ）に
おいて、炭化物析出による２次硬化と、Ｎ１−Ａ Ｉｔ
の金属間化合物析出による析出強化を利用したところに
ある。一般に２次硬化や析出強化を出現させるためには
、合金元素を十分に固溶させるため焼入れ処理や溶体化
処理が必要となる。しかしこのような処理ではマルテン
サイト変態による硬化や固溶強化が生じるだけでなく、
ある程度の焼もどしを行なっても十分な硬度低下は望め
ない。このため本発明ではベイナイト焼入れを採用し、
またこれに適した成分組成を勘案したものである。The present invention contains C0.12 to 0.3%, Si 1% or less, Mn 1% or less, Ni 1.5 to 4.0%, Cr00 in weight%.
8-3.0%, Mo0.5-2.0%, /j20.8-
This is a light alloy forming tool steel characterized by containing 2.0% Fe and the remainder consisting of Fe and inevitable impurity elements. The features of the present invention are secondary hardening due to carbide precipitation and N1-A It at nitriding temperature (520 to 560°C).
This method utilizes precipitation strengthening due to the precipitation of intermetallic compounds. Generally, in order to produce secondary hardening or precipitation strengthening, quenching or solution treatment is required to sufficiently dissolve alloying elements. However, such treatment not only causes hardening and solid solution strengthening due to martensitic transformation, but also
Even if a certain degree of tempering is performed, a sufficient reduction in hardness cannot be expected. For this reason, the present invention adopts bainitic hardening,
In addition, the composition of ingredients suitable for this purpose has been taken into consideration.
ベイナイト焼入れは、オーステナイト化温度から３００
〜４００°Ｃの温度に急冷しこの温度で恒温変態（ベイ
ナイト化）させるものである。この状態では、硬さが低
いにもかかわらず、溶質元素は十分に固溶しており、窒
化温度において、炭化物や金属間化合物を析出させて硬
化するのである。Bainitic quenching is 300° below the austenitizing temperature.
It is rapidly cooled to a temperature of ~400°C and subjected to isothermal transformation (bainite formation) at this temperature. In this state, although the hardness is low, the solute elements are sufficiently dissolved in solid solution, and at the nitriding temperature, carbides and intermetallic compounds are precipitated and hardened.
次”に各元素の限定理由について述べる。Next, we will discuss the reasons for limiting each element.
Ｃは、鋼の強度に必須の元素である。本発明鋼において
は、ベイナイト処理後の低硬度を実現するためにＣはよ
り少ない方が望ましいが、Ｃｒやパ〇の炭化物析出によ
る２次硬化を出現させるためには、少なくとも０．１２
％以上必要である。しかし０、３％を越えるとベイナイ
ト処理による硬さがＨＲＣ４０以下にならないためにＣ
は０．１２〜０．３％とした。C is an essential element for the strength of steel. In the steel of the present invention, in order to achieve low hardness after bainite treatment, it is desirable to have a smaller amount of C, but in order to cause secondary hardening due to carbide precipitation of Cr and P〇, at least 0.12
% or more is required. However, if it exceeds 0.3%, the hardness due to bainite treatment will not go below HRC40, so C
was set at 0.12 to 0.3%.
Ｓｉ、 Ｍｎは、通常脱酸剤や脱硫剤として添加される
ものであり、本発明においては、特に上限のみを規定し
た。これは、それぞれ１％を越えてくると熱間の加工性
を劣化させたり、また非金属介在物として鋼中に残存す
る量が増し、機械的性質を低下させるために上限をそれ
ぞれ１％以下とした。Si and Mn are usually added as deoxidizing agents and desulfurizing agents, and in the present invention, only the upper limit is specified. If each exceeds 1%, hot workability deteriorates, and the amount of nonmetallic inclusions remaining in the steel increases, reducing mechanical properties, so the upper limit is set at 1% or less for each. And so.
Ｃｒは、窒素との親和性が強く、窒化物を形成し窒化層
の強度確保に必須の元素であり、このためには、少なく
とも０．８％以上必要である。しかし３．０％以上にな
ると、ベイナイト処理を行なっても硬さが低下しにくく
なるためにＣｒは０．８〜３．０％とした。Cr has a strong affinity with nitrogen and is an essential element for forming nitrides and ensuring the strength of the nitride layer, and for this purpose, at least 0.8% or more is required. However, when the content of Cr exceeds 3.0%, the hardness becomes difficult to decrease even if bainite treatment is performed, so the content of Cr is set at 0.8 to 3.0%.
ＭＯは２次硬化の必須元素であり、Ｃ量とのバランスか
ら０．５％以上添加しないと効果が得られない。しかし
２．０％を越えるとベイナイト処理後の硬さ低下を困難
にするためにＭｏは０．５〜２．０％とした。MO is an essential element for secondary hardening, and from the balance with the amount of C, no effect can be obtained unless it is added in an amount of 0.5% or more. However, if Mo exceeds 2.0%, it becomes difficult to reduce the hardness after bainitic treatment, so Mo is set at 0.5 to 2.0%.
Ｎｉ、 Ａ１．は窒化処理温度でＮ１５Ａ Ｉｔの金属
間化合物を生成し、微細に析出して高い硬さが得られる
ため本発明鋼において重要な元素である。またＡ２は窒
素との親和性が最も強い元素であり、窒化層中にＡｌＮ
を微細に析出することにより、耐摩耗性に寄与する。こ
れらにＮｉ １．５％、Ａｌ２Ｏ，８％以上は必要であ
るがＮｉ４．０％、ＡＮ２．０％を越えるとＮｉ、Ａｌ
ｌ！の金属間化合物が多量に析出して靭性を低下させる
ためにＮｉは１．５〜４．０％、ＡＮは０．８〜２．０
％とした。Ni, A1. is an important element in the steel of the present invention because it forms an intermetallic compound of N15A It at the nitriding temperature and is finely precipitated to obtain high hardness. In addition, A2 is the element with the strongest affinity for nitrogen, and the nitride layer contains AlN.
contributes to wear resistance by finely precipitating. These require Ni 1.5%, Al2O, 8% or more, but if Ni exceeds 4.0% and AN2.0%, Ni, Al
l! Ni is 1.5 to 4.0% and AN is 0.8 to 2.0% in order to precipitate a large amount of intermetallic compounds and reduce toughness.
%.
以上述べた成分を有する鋼材はベイナイト焼入処理が施
された後需要家に供給される。従って、需要家において
はこの鋼材を容易に型加工ができ、しかも窒化処理を施
すと母材も同時に硬化するのでそのまま使用できるため
、大幅な工程短縮を可能にするだけでなく型の設計変更
に対しても機敏に対応することができる。Steel materials having the above-mentioned components are supplied to customers after being subjected to bainitic quenching treatment. Therefore, customers can easily process this steel into molds, and since the base metal is hardened at the same time when nitriding is applied, it can be used as is.This not only makes it possible to significantly shorten the process, but also allows for changes in mold design. You can also respond quickly.
第１表に示す本発明鋼および比較鋼に用いたＳ［１６１
の性能および使用実績について述べる。S[161
This section describes the performance and usage history of the system.
第１図に各供試材の焼もどし硬さを示した。Figure 1 shows the tempering hardness of each sample material.
Ｅ−１は５ＫＤ６１を１０００℃から油冷した場合の焼
もどし曲線である。この場合、型加工が容易なように約
６５０ ’Ｃの高温焼もどしが施され、需要家に供給さ
れるが、すでに軟化域であり、窒化処理による軟化や、
使用中の摩擦による上昇により型は十分な母材強度を確
保することができない。Ｅ−２は５ＫＤ６１を１０００
°Ｃからベイナイト焼入した場合である。５ＫＤ６１は
Ｃ，Ｃｒ９１が高く、焼入ままの状態でも十分な低硬度
ま得られず、また２次硬化の程度も低い。Ａ−Ｄは１０
００°Ｃから３８０°Ｃにベイナイト焼入し、この温度
で恒温変態させたものである。焼入ままでＩＩＲＣ４０
以下であり、２次硬化（焼もどし時間２時間の場合）に
おいてＩＩＲＣ４０以上となる。このように需要家に納
入された状態では、機械加工が容易な低硬度を実現して
いる。第２図は窒化処理を行なった場合の硬さ変化を見
るため、５４０°Ｃでの硬さと保持時間の関係を示した
ものである。本発明鋼はＮｉ、Ａ ４２の析出によりし
だいに硬化している。これに対しベイナイト焼入した５
ＫＤ６１ （Ｅ−２）は、保持時間とともに軟化してい
るのがわかる。本発明鋼は、長時間の保持においても硬
化の傾向が見られる。これを実用面からみると型がある
程度摩耗した場合再研削、再窒化処理して使用しても、
型の内部硬さを維持できることを示している。第２表は
、Ａ２押出ダイスとして使用した例である。５ＫＤ６１
はＣｒ、 Ｍｏを含み比較的高い硬さの窒化層が得られ
るものの内部硬さが低く、また使用中に軟化してくるた
め、型のへクリにより寿命となっている。本発明ｍＡ−
Ｄは、硬質の窒化層を得るのに最も有効な元素であるＡ
ｊ２゜Ｃａ、 Ｍｏを含有しているため、高い窒化層硬
さが得られており、しかも内部硬さも高い値を示してい
る。いずれも６０００ｋｇの押出量でも異常なく使用す
ることができる。E-1 is a tempering curve when 5KD61 is oil-cooled from 1000°C. In this case, it is tempered at a high temperature of approximately 650'C to facilitate mold processing and is supplied to customers, but it is already in the softened region and may be softened by nitriding.
Due to the rise caused by friction during use, the mold cannot ensure sufficient strength of the base material. E-2 is 5KD61 for 1000
This is the case of bainitic hardening from °C. 5KD61 has a high C and Cr91 content, and even in the as-quenched state, a sufficiently low hardness cannot be obtained, and the degree of secondary hardening is also low. A-D is 10
It is bainitic hardened from 00°C to 380°C and subjected to isothermal transformation at this temperature. IIRC40 as quenched
and the second hardening (tempering time of 2 hours) results in an IIRC of 40 or more. In this way, in the state delivered to the customer, it has a low hardness that makes machining easy. Figure 2 shows the relationship between hardness at 540°C and holding time in order to see changes in hardness when nitriding is performed. The steel of the present invention gradually hardens due to the precipitation of Ni and A42. On the other hand, bainite-quenched 5
It can be seen that KD61 (E-2) softens as the holding time increases. The steel of the present invention shows a tendency to harden even when held for a long time. From a practical point of view, if the mold is worn to some extent, even if it is re-grinded and re-nitrided before use,
This shows that the internal hardness of the mold can be maintained. Table 2 shows an example of use as an A2 extrusion die. 5KD61
Although it contains Cr and Mo and provides a nitrided layer with relatively high hardness, its internal hardness is low and it softens during use, so its life is limited by mold damage. The present invention mA-
D is A, which is the most effective element for obtaining a hard nitrided layer.
Since it contains Ca and Mo, a high nitrided layer hardness is obtained, and the internal hardness also shows a high value. Both can be used without any abnormality even at an extrusion amount of 6000 kg.
本発明は、従来の軽合金成形用工具鋼において懸案であ
った、型製造工数の短縮と型寿命向上の問題を一度に解
決したものであり、型加工時は低硬度であり、窒化処理
において硬質の窒化層と十分な内部強度が達成できるの
でその工業的意義は大きい。The present invention solves the problems of shortening mold manufacturing man-hours and improving mold life, which were concerns with conventional light alloy forming tool steels. It has great industrial significance because it can achieve a hard nitrided layer and sufficient internal strength.
第１図は、供試材の焼もどし硬さを示すグラフ、第２図
は、供試材を焼入後５４０°Ｃで保持した場合の時間と
硬さの関係を示すグラフである。
第１図
焼もどし温度（℃Ｘ２ｈ空冷）
第２図
保持時間（Ｈｒ）FIG. 1 is a graph showing the tempering hardness of the test material, and FIG. 2 is a graph showing the relationship between time and hardness when the test material is held at 540° C. after quenching. Figure 1 Tempering temperature (°C x 2h air cooling) Figure 2 Holding time (Hr)
Claims (1)
％以下、Ｎｉ１．５〜４．０％、Ｃｒ０．８〜３．０％
、Ｍｏ０．５〜２．０％、Ａｌ０．８〜２．０％を含み
、残部Ｆｅおよび不可避的不純物元素からなることを特
徴とする軽合金成形用工具鋼。C0.12-0.3% by weight, Si1% or less, Mn1
% or less, Ni1.5-4.0%, Cr0.8-3.0%
, 0.5 to 2.0% of Mo, and 0.8 to 2.0% of Al, with the balance consisting of Fe and inevitable impurity elements.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62258720A JP2655848B2 (en) | 1987-10-14 | 1987-10-14 | Tool steel for forming light alloys |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62258720A JP2655848B2 (en) | 1987-10-14 | 1987-10-14 | Tool steel for forming light alloys |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH01104749A true JPH01104749A (en) | 1989-04-21 |
| JP2655848B2 JP2655848B2 (en) | 1997-09-24 |
Family
ID=17324153
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP62258720A Expired - Lifetime JP2655848B2 (en) | 1987-10-14 | 1987-10-14 | Tool steel for forming light alloys |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2655848B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP2662462A1 (en) | 2012-05-07 | 2013-11-13 | Valls Besitz GmbH | Low temperature hardenable steels with excellent machinability |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61110751A (en) * | 1984-11-02 | 1986-05-29 | Plus Eng Co Ltd | Knockout pin having superior toughness |
-
1987
- 1987-10-14 JP JP62258720A patent/JP2655848B2/en not_active Expired - Lifetime
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61110751A (en) * | 1984-11-02 | 1986-05-29 | Plus Eng Co Ltd | Knockout pin having superior toughness |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP2662462A1 (en) | 2012-05-07 | 2013-11-13 | Valls Besitz GmbH | Low temperature hardenable steels with excellent machinability |
| WO2013167580A1 (en) | 2012-05-07 | 2013-11-14 | Valls Besitz Gmbh | Low temperature hardenable steels with excellent machinability |
| US10077490B2 (en) | 2012-05-07 | 2018-09-18 | Valls Besitz Gmbh | Low temperature hardenable steels with excellent machinability |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2655848B2 (en) | 1997-09-24 |
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