JPH01111846A - Hot-working tool - Google Patents
Hot-working toolInfo
- Publication number
- JPH01111846A JPH01111846A JP26924787A JP26924787A JPH01111846A JP H01111846 A JPH01111846 A JP H01111846A JP 26924787 A JP26924787 A JP 26924787A JP 26924787 A JP26924787 A JP 26924787A JP H01111846 A JPH01111846 A JP H01111846A
- Authority
- JP
- Japan
- Prior art keywords
- weight
- hot
- nitriding
- tool steel
- work tool
- 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.)
- Pending
Links
- 229910001315 Tool steel Inorganic materials 0.000 claims description 24
- 238000005121 nitriding Methods 0.000 abstract description 32
- 229910052782 aluminium Inorganic materials 0.000 abstract description 8
- 238000004512 die casting Methods 0.000 abstract description 7
- 238000009826 distribution Methods 0.000 abstract description 7
- 239000000203 mixture Substances 0.000 abstract description 6
- 229910052748 manganese Inorganic materials 0.000 abstract description 3
- 229910000717 Hot-working tool steel Inorganic materials 0.000 abstract 3
- 229910052799 carbon Inorganic materials 0.000 abstract 2
- 229910052804 chromium Inorganic materials 0.000 abstract 2
- 229910052710 silicon Inorganic materials 0.000 abstract 2
- 229910052720 vanadium Inorganic materials 0.000 abstract 2
- 238000004519 manufacturing process Methods 0.000 abstract 1
- 229910052750 molybdenum Inorganic materials 0.000 abstract 1
- 229910052721 tungsten Inorganic materials 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 13
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 6
- 229910045601 alloy Inorganic materials 0.000 description 5
- 239000000956 alloy Substances 0.000 description 5
- 150000001247 metal acetylides Chemical class 0.000 description 5
- 238000000034 method Methods 0.000 description 4
- 229910000831 Steel Inorganic materials 0.000 description 3
- 239000002131 composite material Substances 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 239000000523 sample Substances 0.000 description 3
- 239000010959 steel Substances 0.000 description 3
- 230000007423 decrease Effects 0.000 description 2
- 150000004767 nitrides Chemical class 0.000 description 2
- 229910052761 rare earth metal Inorganic materials 0.000 description 2
- 238000005496 tempering Methods 0.000 description 2
- 238000005266 casting Methods 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000001192 hot extrusion Methods 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- 238000010301 surface-oxidation reaction Methods 0.000 description 1
Landscapes
- 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、窒化処理特性の優れた熱間工具鋼に関する。[Detailed description of the invention] Industrial applications The present invention relates to hot work tool steel with excellent nitriding properties.
従来の技術
従来、ＡＩダイカストスリーブ等、熱間工具には、５Ｋ
Ｏ−６１等の合金工具鋼を窒化処理して使用されている
。アルミニウムのダイカストスリーブにおいては、溶融
アルミニウムにより繰り返し熱衝撃的な作用を受けるの
で、その影響により窒化層が溶損していき、工具鋼とし
ての寿命が尽きてしまう、その為に強靭で高温特性の優
れた窒化層を有するものが望まれている。Conventional technology Conventionally, hot tools such as AI die-casting sleeves require 5K
Alloy tool steel such as O-61 is used after being nitrided. Aluminum die-cast sleeves are subjected to repeated thermal shock effects from molten aluminum, which causes the nitride layer to melt and wear away, ending the life of the tool steel. It is desired to have a nitrided layer.
発明が解決しようとする間怠点
ところで、従来使用されている５ＫＤ−６１等の合金工
具鋼は、通常５００〜５５０℃で５ｏ〜１００時間、ガ
ス窒化法による二段窒化処理によって窒化が行われてい
るが、窒化層の厚さ、即ち窒化深さは０．２〜０６３−
程度にとどまり、したがって又、硬さも窒化層表面から
内部に向かって急激に変化するものとなっていた。した
がって、例えばＡＩダイカスト用ススリーブして使用し
た場合、溶ＭｉＡＩによる熱影響で、ヒートチエツクを
生じ、窒化層の剥離ないしは溶損が容易に起るという閉
頭があった。又、窒化条件を変更して、窒化深さを深く
しようとすると、ε相の析出による過剰窒化になりやす
いという閉頭があり、窒化深さを上記の深さ以上に増大
させることは困難であった。したがって、窒化処理した
場合に十分な膜厚の窒化層が形成され、硬さの分布もな
だらかに変化するような熱間工具鋼の出現が望まれてい
た。By the way, conventionally used alloy tool steels such as 5KD-61 are usually nitrided by a two-stage nitriding process using a gas nitriding method at 500 to 550°C for 50 to 100 hours. However, the thickness of the nitrided layer, that is, the nitrided depth, is 0.2 to 0.63 -
Therefore, the hardness also changed rapidly from the surface of the nitrided layer toward the inside. Therefore, when used as a sleeve for AI die casting, for example, a heat check occurs due to the thermal influence of the molten MiAI, and the nitride layer easily peels off or melts away. In addition, if you try to increase the nitriding depth by changing the nitriding conditions, there is a problem that excessive nitriding tends to occur due to the precipitation of the ε phase, and it is difficult to increase the nitriding depth beyond the above-mentioned depth. there were. Therefore, it has been desired to develop a hot work tool steel in which a sufficiently thick nitrided layer is formed when nitrided and the hardness distribution changes smoothly.
本発明は、従来の上記のような事情の下になされたもの
である。The present invention has been made under the above-mentioned conventional circumstances.
したがって、本発明の目的は、窒化処理を行なった場合
に、窒化深さが深く、硬さ分布がなだらかで、緻密な窒
化層を形成することができる熱間工具鋼を提供すること
にある。Therefore, an object of the present invention is to provide a hot work tool steel that has a deep nitriding depth, a gentle hardness distribution, and can form a dense nitrided layer when subjected to nitriding treatment.
本発明の他の目的は、アルミニウム等の熱開成形におい
て、寿命の長い熱間工具鋼を提供することにある。Another object of the present invention is to provide a hot work tool steel that has a long life in hot open forming of aluminum and the like.
問題点を解決するための手段
本発明者等は、鋭意検討の結果、従来使用されている熱
間工具鋼に、所定量のアルミニウムを含有させると、上
記の目的が達成されることを見出だし、本発明を完成す
るに至った。Means for Solving the Problems As a result of intensive studies, the inventors of the present invention have found that the above object can be achieved by adding a predetermined amount of aluminum to the hot work tool steel that has been used in the past. , we have completed the present invention.
本発明の熱間工具鋼は、Ｃ： ０．２〜１，２重量％；
Ｓｉ：０．０５〜２重量％； Ｍ ｎ ： Ｏ−０５〜
２重量％；Ｃｒ：２〜１５重量％； Ｗ＋１／２ Ｍ
ｏ ： ０．２〜１２重量％；Ｖ：０．１〜５重量％；
、Ａｌ ：０．１〜１．５重量％；及び残部Ｆｅから
なることを特徴とする。The hot work tool steel of the present invention contains C: 0.2 to 1.2% by weight;
Si: 0.05~2% by weight; Mn: O-05~
2% by weight; Cr: 2-15% by weight; W+1/2 M
o: 0.2 to 12% by weight; V: 0.1 to 5% by weight;
, Al: 0.1 to 1.5% by weight; and the remainder Fe.
本発明の熱間工具鋼は、快削性を増すなめに、上記の合
金組成に更にＳ ： ０．０３〜０．３重量％を含有さ
せるのが好ましい。The hot work tool steel of the present invention preferably contains 0.03 to 0.3% by weight of S in the above alloy composition in order to increase free machinability.
以下、本発明の熱間工具鋼に就いて詳細に説明する。Hereinafter, the hot work tool steel of the present invention will be explained in detail.
本発明における熱間工具鋼の成分範囲の限定理由は、次
の通りである。The reason for limiting the composition range of the hot work tool steel in the present invention is as follows.
Ｃ： ０．２〜１．２重量％
Ｃは、炭化物形成元素と結合して硬い複合炭化物を生成
し、熱間工具鋼として熱間強度、靭性、耐磨耗性等の性
質を確保するのに必要な元素であり、そのような効果を
発揮させるために０．２重量％以上含有させることが必
要である。又、Ｃの量が１．２重量％を超えると靭性の
低下が著しくなるので、上１は１．２重量％に設定する
必要がある。C: 0.2 to 1.2% by weight C combines with carbide-forming elements to form hard composite carbides, ensuring properties such as hot strength, toughness, and wear resistance as hot work tool steel. It is an element necessary for this, and in order to exhibit such an effect, it is necessary to contain it in an amount of 0.2% by weight or more. Further, if the amount of C exceeds 1.2% by weight, the toughness decreases significantly, so the above 1 needs to be set at 1.2% by weight.
Ｓ ｉ ： ０．０５〜２重量％
Ｓｉは主に脱酸剤として作用し、また焼入性を向上させ
ると共に基地を強化して降伏点を高め、高温度での表面
酸化を阻止するのに有効な元素であるが、０．０５重量
％よりも少ないと、その効果が発揮されがたい。又、２
重量％を超えると、靭性の低下が著しくなる。Si: 0.05 to 2% by weight Si mainly acts as a deoxidizing agent, and also improves hardenability, strengthens the base, increases the yield point, and prevents surface oxidation at high temperatures. Although it is an effective element, if it is less than 0.05% by weight, it is difficult to exhibit its effect. Also, 2
If it exceeds % by weight, the toughness will be significantly reduced.
Ｍ ｎ ； ｏ、ｃｓ−２重１％
Ｍｎは、主に脱酸剤として作用し、羽の清浄度を高める
と共に、焼入性の向上にも寄与する元素であるので、そ
のような効果を得るために０．０５重量％以上添加する
必要がある。しかしながら、その添加量が多すぎると熱
間加工性が低下するので、上限は２重量％以下に設定す
ることが必要である。Mn; o, cs-2 wt 1% Mn is an element that mainly acts as a deoxidizing agent and improves the cleanliness of the blade and also contributes to improving the hardenability. It is necessary to add 0.05% by weight or more to obtain this. However, if the amount added is too large, hot workability will deteriorate, so it is necessary to set the upper limit to 2% by weight or less.
Ｃｒ ：２〜１５重量％
ＣｒはＣと結合して複合炭化物を形成し、工具鋼の焼入
性や焼戻硬さを高め、高温強度の向上に有効であり、最
も重要な含有元素であるが、２重量％未満では効果が小
さく、一方、１５重量％を超えると粗大な炭化物を生じ
る。Cr: 2-15% by weight Cr combines with C to form composite carbides, increases the hardenability and tempering hardness of tool steel, and is effective in improving high-temperature strength, and is the most important element included. However, if it is less than 2% by weight, the effect is small, while if it exceeds 15% by weight, coarse carbides are produced.
Ｗ＋ １／２ Ｍ ｏ ： ０．２〜１２重１重量％は
、焼入性、焼戻軟化抵抗や高温強度の向上に寄与が大き
く、窒化特性向上の効果も顕著な元素である。又はＷは
、焼入性は窒化特性への影響は小さいが、それ以外の特
性面はＭｏとほぼ同じ影響を及ぼす重要な元素である。W+ 1/2 Mo: 0.2 to 12% by weight is an element that greatly contributes to improving hardenability, temper softening resistance, and high temperature strength, and also has a remarkable effect of improving nitriding properties. Alternatively, W is an important element that has a small effect on hardenability on nitriding properties, but has almost the same effect as Mo on other properties.
Ｗ ＋ １／２ Ｍ 。W + 1/2 M.
の合計量が０．２重量％より低いと、アルミニウムダイ
カスト用スリーブにとっての効果が小さく、１２重量％
を超えると靭性低下が著しくなるので、上記の範囲に設
定する。If the total amount is lower than 0.2% by weight, the effect on the sleeve for aluminum die casting will be small;
If it exceeds this, the toughness will deteriorate significantly, so it is set within the above range.
Ｖ：０．１〜５重量％
■はＣと結合してｙ＆細な複合炭化物を形成し、焼入結
晶粒の粗大化防止効果を示し、高硬質の炭化物として残
留し、高温強度や耐ｒ！Ｊ粍性の向上に寄与するが、０
．１重１％より低いと、その効果が小さく、一方、５重
量％を超えると粗大な炭化物が増大し、被切削性や靭性
の低下が著しくなる。V: 0.1 to 5% by weight ■ combines with C to form y&fine composite carbides, exhibits the effect of preventing coarsening of quenched crystal grains, remains as a highly hard carbide, and improves high temperature strength and r resistance. ! Although it contributes to improving J
．． If it is less than 1% by weight, the effect will be small, while if it exceeds 5% by weight, coarse carbides will increase, resulting in a significant decrease in machinability and toughness.
Ａｌ：０．１〜１．５重量％
ＡＩは、窒化深さや・窒化層の硬さ分布に最も効果的に
影響を及ぼす元素であるが、０．１重１％より低いとそ
の効果が少なく、一方、１．５重量％を超えると、靭性
や熱間加工性が著しく低下する。Al: 0.1 to 1.5% by weight Al is the element that most effectively affects the nitriding depth and hardness distribution of the nitrided layer, but if it is lower than 0.1% by weight, its effect is small. On the other hand, when it exceeds 1.5% by weight, toughness and hot workability are significantly reduced.
Ｓ ： ０．０３〜０．３重量％
Ｓは、主にＭｎと結合してＭ ｎ Ｓを形成し、強度及
び靭性を低下させるので、Ｓ含有量は低い方が望ましい
。しかしながら、成形加工時の被剛性が重視される場合
には、被剛性を確保する上で、下限を０．０３重量％、
上限を０．３重量％に設定する。S: 0.03 to 0.3% by weight S mainly combines with Mn to form MnS and reduces strength and toughness, so a lower S content is desirable. However, if rigidity during molding is important, the lower limit should be 0.03% by weight to ensure rigidity.
The upper limit is set at 0.3% by weight.
本発明の熱間工具鋼は、上記の組成を有することが特徴
であるが、更に、窒化速度を更に高めるために、所望に
よっては、Ｔ ｉ ： ０．０１〜１重量％を含有させ
てもよい。The hot work tool steel of the present invention is characterized by having the above-mentioned composition, but may also contain Ti: 0.01 to 1% by weight, if desired, in order to further increase the nitriding rate. good.
更に又、本発明の熱間工具鋼において、被剛性が重要視
される場合には、Ｓと共に希土類元素、Ｃａ、Ｍｇ、Ｚ
ｒよりなる群から選択された１種又は２種以上を含有さ
せてもよい。その場合、希土類元素は０．０５〜０．２
重１％、Ｃａは０．００１〜ｏ、ｉ重量％、Ｍｇは０．
０５〜２重量％、Ｚｒは０．０５〜２重量％の範囲で含
有させるのが好ましい。Furthermore, in the hot work tool steel of the present invention, when rigidity is important, rare earth elements, Ca, Mg, Z are added in addition to S.
One or more selected from the group consisting of r may be included. In that case, the rare earth element is 0.05-0.2
Weight: 1%, Ca: 0.001-0, i weight%: Mg: 0.
Zr is preferably contained in a range of 0.05 to 2% by weight.
作用
本発明の熱間工具鋼は、上記のように所定量のＡＩが含
有されているから、窒化深さが深く、かつ、なだらかな
硬さ分布を示す、これを第１図によって説明する。第１
図は、後記実施例の恥２、ＮＯ３及びＮＯ３の熱間工具
鋼と、ＮＯ３の５ＫＤ６１とについて、同じ条件で窒化
処理した場合における、表面からの距離とビッカース硬
さとの関係を示すものである。Function: Since the hot work tool steel of the present invention contains a predetermined amount of AI as described above, it has a deep nitriding depth and exhibits a gentle hardness distribution. This will be explained with reference to FIG. 1. 1st
The figure shows the relationship between the distance from the surface and the Vickers hardness when nitriding the hot work tool steels 2, NO3, and NO3 of Examples described later and 5KD61 of NO3 under the same conditions. .
第１図から明らかなように、本発明の熱間工具鋼は、Ａ
Ｉが含有されることによって、硬さの分布が表面から内
部に向かってなだらかな傾斜をなしており、窒化深さは
、同じ窒化処理条件で処理した、従来の５ＫＤ６１にお
ける窒化深さの約２倍にもなる。As is clear from FIG. 1, the hot work tool steel of the present invention is A
Due to the inclusion of I, the hardness distribution forms a gentle slope from the surface to the inside, and the nitriding depth is approximately 2 times the nitriding depth of conventional 5KD61 treated under the same nitriding conditions. It will double.
実施例 次に、本発明を実施例によって説明する。Example Next, the present invention will be explained by examples.
Ｆｅ以外の成分が下記第１表に示す合金組成よりなる２
００ ｋｇ鋼塊を、真空誘電ｆにより溶製し、厚さ２０
市の板に鍛伸した後、常法により焼ならし、焼なまし、
焼入れ、焼戻しを順次行って供試材を得た。2 whose components other than Fe consist of the alloy composition shown in Table 1 below
A 00 kg steel ingot was melted using a vacuum dielectric f to a thickness of 20 kg.
After being forged into a commercial board, it is normalized, annealed, and
A test material was obtained by sequentially quenching and tempering.
この供試材を５００〜５５０℃の温度で７０時面間常法
のガス窒化法により二段窒化処理を行なった。This sample material was subjected to two-stage nitriding treatment using a conventional gas nitriding method at a temperature of 500 to 550° C. for 70 hours.
それぞれの供試材について、窒化処理後の表面のビッカ
ース硬さ及び窒化深さを第１表に示す。Table 1 shows the Vickers hardness and nitriding depth of the surface of each sample material after nitriding.
又、上記の合金組成の熱間工具鋼を、同様に窒化処理を
施して得られたＡｌダイカスト用スリーブを用い、溶融
アルミニウムを鋳造温度６００〜７００℃で熱間処理し
、Ａ！ダイカスト用ススリーブ寿命を調査した。その結
果もまた第１表に示す。Further, using an Al die casting sleeve obtained by similarly nitriding hot work tool steel having the above alloy composition, molten aluminum was hot treated at a casting temperature of 600 to 700°C, and A! The lifespan of sleeves for die casting was investigated. The results are also shown in Table 1.
尚、寿命は、従来の５ＫＤ−６１を１とした場合の指数
で示す。Note that the life span is expressed as an index when the conventional 5KD-61 is set as 1.
更にＮａ３、ＮＱ ３、ＮＱ６及び■７の供試材につい
て、それ等の表面のビッカース硬さと表面からの距離と
の関係を調査しな、その結果を第１図に示す。Furthermore, the relationship between the Vickers hardness of the surface and the distance from the surface was investigated for the sample materials Na3, NQ3, NQ6 and 7. The results are shown in FIG.
これ等の供試材を８５０℃で５０時間加熱した後、同様
にビッカース硬さと表面からの距離との関係を調査した
。その結果を第２図に示す。After heating these test materials at 850° C. for 50 hours, the relationship between Vickers hardness and distance from the surface was similarly investigated. The results are shown in FIG.
これ等の結果から、本発明の熱間工具鋼は、窒化深さが
深く、又、熱間処理による劣化が少ないことが分かる。From these results, it can be seen that the hot work tool steel of the present invention has a deep nitriding depth and less deterioration due to hot treatment.
発明の効果
本発明の熱間工具鋼は、窒化特性が極めて良好であり、
窒化処理により窒化深さが著しく深く、かつ硬さ分布が
なだらかな、緻密な窒化層が形成される。したがって、
本発明の熱間工具鋼を用いて作成された熱間工具は、使
用中、例えば、溶融ＡＩにより繰返し熱影響を受けても
、軟化或いはヒートチエツクを生じ難くなり、窒化層の
剥離ないしは溶損が起り難くなり、したがって又、寿命
も長いものとなる。Effects of the Invention The hot work tool steel of the present invention has extremely good nitriding properties,
The nitriding process forms a dense nitrided layer with a significantly deep nitriding depth and a gentle hardness distribution. therefore,
Hot work tools made using the hot work tool steel of the present invention are less susceptible to softening or heat checks even when subjected to repeated thermal effects, for example due to molten AI, during use, resulting in peeling or melting damage of the nitrided layer. It is less likely that this will occur, and therefore the lifespan will be longer.
本発明の熱間工具鋼は、特にＡＩダイカスト用ススリー
ブＡＩ熱間押出し用マンドレル、ダミーブロック等に適
しているが、その他の熱間処理用工具、例えば熱間加工
用金型等にも適用できる。The hot work tool steel of the present invention is particularly suitable for AI die casting sleeves, AI hot extrusion mandrels, dummy blocks, etc., but can also be applied to other hot processing tools, such as hot working molds, etc. .
第１図は、窒化処理した熱間工具鋼のビッカース硬度と
表面からの距離との関係を示すグラフであり、第２図は
、窒化処理した後、熱処理した場合におけるビッカース
硬度と表面からの距離との関係を示すグラフである。
特許出願人 大同特殊鋼株式会社
代理人 弁理士 渡部 剛
０．５ ’、０ １．５ ２
．０表面からの距離（駅）
０．５ １．０ １．５ ２
．Ｃ’表面からの距離（＃Ｉ）Figure 1 is a graph showing the relationship between Vickers hardness and distance from the surface of nitrided hot work tool steel, and Figure 2 is a graph showing the relationship between Vickers hardness and distance from the surface when heat treated after nitriding. It is a graph showing the relationship between Patent applicant Daido Steel Co., Ltd. Agent Patent attorney Tsuyoshi Watanabe 0.5', 0 1.5 2
．． 0 Distance from surface (station) 0.5 1.0 1.5 2
．． Distance from C' surface (#I)
Claims (2)
重量％；Ｍｎ：０．０５〜２重量％；Ｃｒ：２〜１５重
量％；Ｗ＋１／２Ｍｏ：０．２〜１２重量％；Ｖ：０．
１〜５重量％；；Ａｌ：０．１〜１．５重量％；及び残
部Ｆｅからなることを特徴とする熱間工具鋼。(1) C: 0.2-1.2% by weight; Si: 0.05-2
Weight %; Mn: 0.05-2 weight %; Cr: 2-15 weight %; W+1/2Mo: 0.2-12 weight %; V: 0.
A hot work tool steel comprising: 1 to 5% by weight; Al: 0.1 to 1.5% by weight; and the balance Fe.
重量％；Ｍｎ：０．０５〜２重量％；Ｃｒ：２〜１５重
量％；Ｗ＋１／２Ｍｏ：０．２〜１２重量％；Ｖ：０．
１〜５重量％；Ｓ：０．０３〜０．３重量％；Ａｌ：０
．１〜１．５重量％；及び残部Ｆｅからなることを特徴
とする熱間工具鋼。(2) C: 0.2-1.2% by weight; Si: 0.05-2
Weight %; Mn: 0.05-2 weight %; Cr: 2-15 weight %; W+1/2Mo: 0.2-12 weight %; V: 0.
1-5% by weight; S: 0.03-0.3% by weight; Al: 0
．． 1 to 1.5% by weight; and the balance Fe.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP26924787A JPH01111846A (en) | 1987-10-27 | 1987-10-27 | Hot-working tool |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP26924787A JPH01111846A (en) | 1987-10-27 | 1987-10-27 | Hot-working tool |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH01111846A true JPH01111846A (en) | 1989-04-28 |
Family
ID=17469694
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP26924787A Pending JPH01111846A (en) | 1987-10-27 | 1987-10-27 | Hot-working tool |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH01111846A (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0648852A1 (en) * | 1993-09-27 | 1995-04-19 | Crucible Materials Corporation | Hot-isostatically-compacted martensitic steel article for molds and die components and its method of manufacture |
| KR20010046367A (en) * | 1999-11-12 | 2001-06-15 | 이구택 | Method for Manufacturing Tool Steel |
| KR100331962B1 (en) * | 1996-05-08 | 2002-11-27 | 기아특수강 주식회사 | Method for manufacturing high cleanliness tool steel with improved macro/micro-solidification structure |
| CN100357477C (en) * | 2005-07-06 | 2007-12-26 | 燕山大学 | Super bainite abrasion-resistant steel and its manuafcturing process |
| US7387692B2 (en) * | 2006-01-09 | 2008-06-17 | Ati Properties, Inc. | Tool and bearing steels |
| US7655101B2 (en) * | 2006-10-27 | 2010-02-02 | Boehler Edelstahl Gmbh | Steel alloy for cutting tools |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS53149808A (en) * | 1977-05-06 | 1978-12-27 | Hitachi Metals Ltd | Abrasionnresistant steel for nitriding use |
-
1987
- 1987-10-27 JP JP26924787A patent/JPH01111846A/en active Pending
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS53149808A (en) * | 1977-05-06 | 1978-12-27 | Hitachi Metals Ltd | Abrasionnresistant steel for nitriding use |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0648852A1 (en) * | 1993-09-27 | 1995-04-19 | Crucible Materials Corporation | Hot-isostatically-compacted martensitic steel article for molds and die components and its method of manufacture |
| KR100331962B1 (en) * | 1996-05-08 | 2002-11-27 | 기아특수강 주식회사 | Method for manufacturing high cleanliness tool steel with improved macro/micro-solidification structure |
| KR20010046367A (en) * | 1999-11-12 | 2001-06-15 | 이구택 | Method for Manufacturing Tool Steel |
| CN100357477C (en) * | 2005-07-06 | 2007-12-26 | 燕山大学 | Super bainite abrasion-resistant steel and its manuafcturing process |
| US7387692B2 (en) * | 2006-01-09 | 2008-06-17 | Ati Properties, Inc. | Tool and bearing steels |
| US7655101B2 (en) * | 2006-10-27 | 2010-02-02 | Boehler Edelstahl Gmbh | Steel alloy for cutting tools |
| EP1918401A3 (en) * | 2006-10-27 | 2012-05-30 | Böhler Edelstahl GmbH & Co KG | Steel alloy for machining tools |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JPH0717986B2 (en) | Alloy tool steel | |
| EP0338133B1 (en) | Steels for hot working press tools | |
| JPH01111846A (en) | Hot-working tool | |
| JPH0555585B2 (en) | ||
| JPH07102342A (en) | Hot tool steel with high toughness | |
| CZ20032755A3 (en) | Tool steel, process for producing parts of such steel and a steel part obtained in such a manner | |
| JP2005187900A (en) | Cold tool steel having excellent surface treatability, component for die, and die | |
| JP2001158937A (en) | Tool steel for hot working, method for producing same and method for producing tool for hot working | |
| JPH10121195A (en) | Hot tool steel excellent in nitriding characteristics | |
| JPH0426739A (en) | Steel for hot tube manufacturing tool and hot tube manufacturing tool thereof | |
| JP2953304B2 (en) | Roll outer tube material for continuous sheet casting machine | |
| JPH0688163A (en) | Hot tool steel | |
| JPH07173571A (en) | High workability wear resistant steel and production thereof | |
| JP2795605B2 (en) | Roll material for continuous casting | |
| US4116685A (en) | Tool steel for warm and hot working | |
| JPS6366384B2 (en) | ||
| JP3191008B2 (en) | Hot tool steel | |
| JPH09227990A (en) | Hot tool steel excellent in high temperature strength and fracture toughness | |
| JP3417922B2 (en) | Cast iron for sizing press die | |
| KR101986187B1 (en) | Cast steel | |
| JPH0718378A (en) | Steel for hot die | |
| JPS5942743B2 (en) | hot work tool steel | |
| JP2678536B2 (en) | Cold tool steel | |
| JPH06248389A (en) | Maraging steel for die casting die | |
| KR830001051B1 (en) | Wrought tool steel for hot working |