JPS62274059A - Free-cutting age-hardening austenitic tool steel - Google Patents
Free-cutting age-hardening austenitic tool steelInfo
- Publication number
- JPS62274059A JPS62274059A JP11818186A JP11818186A JPS62274059A JP S62274059 A JPS62274059 A JP S62274059A JP 11818186 A JP11818186 A JP 11818186A JP 11818186 A JP11818186 A JP 11818186A JP S62274059 A JPS62274059 A JP S62274059A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- tool steel
- free
- age
- hardening
- 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 title claims abstract description 12
- 238000003483 aging Methods 0.000 title claims description 11
- 238000005520 cutting process Methods 0.000 title claims description 5
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 10
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 10
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 7
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 7
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 5
- 229910052710 silicon Inorganic materials 0.000 claims abstract 4
- 239000012535 impurity Substances 0.000 claims description 3
- 239000000203 mixture Substances 0.000 abstract description 6
- 229910052759 nickel Inorganic materials 0.000 abstract description 3
- 229910052742 iron Inorganic materials 0.000 abstract description 2
- 229910052799 carbon Inorganic materials 0.000 abstract 2
- 229910052748 manganese Inorganic materials 0.000 abstract 2
- 229910000831 Steel Inorganic materials 0.000 description 32
- 239000010959 steel Substances 0.000 description 32
- 230000000694 effects Effects 0.000 description 16
- 230000007423 decrease Effects 0.000 description 8
- 229910045601 alloy Inorganic materials 0.000 description 6
- 239000000956 alloy Substances 0.000 description 6
- 230000032683 aging Effects 0.000 description 4
- 238000009864 tensile test Methods 0.000 description 4
- 230000001771 impaired effect Effects 0.000 description 3
- 230000003647 oxidation Effects 0.000 description 3
- 238000007254 oxidation reaction Methods 0.000 description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 239000010949 copper Substances 0.000 description 2
- 238000005553 drilling Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000011081 inoculation Methods 0.000 description 2
- 150000001247 metal acetylides Chemical class 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 239000012086 standard solution Substances 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 238000005496 tempering Methods 0.000 description 2
- 150000003568 thioethers Chemical class 0.000 description 2
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000001125 extrusion Methods 0.000 description 1
- 230000002431 foraging effect Effects 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000009827 uniform distribution Methods 0.000 description 1
Landscapes
- Cutting Tools, Boring Holders, And Turrets (AREA)
Abstract
Description
【発明の詳細な説明】
６ 発明の詳細な説明
〔産業上の利用分野〕
本発明は、従来のオーステナイト熱間工具鋼に比べ、被
剛性が著しく良好でかつ特に高温度での使用に優れた性
能を有するオーステナイト工具鋼に関するものである。[Detailed Description of the Invention] 6 Detailed Description of the Invention [Field of Industrial Application] The present invention provides a tool steel that has significantly better stiffness than conventional austenitic hot work tool steels and is particularly excellent in use at high temperatures. The present invention relates to an austenitic tool steel with high performance.
熱間工具鋼には用途に応じて稽々のものがあり、従来、
アルミニウムおよびこれより溶融点の低い金ＩＩ４また
は合金の熱間加工に対しては、５ＫＤ５゜Ａｌ５Ｉ
ＨＩ３のような高合金熱間ダイス鋼が使用されている。There are different types of hot work tool steel depending on the application, and conventionally,
For hot working of aluminum and lower melting point gold II4 or alloys, 5KD5°Al5I
High alloy hot die steels such as HI3 are used.
また、銅およびその合金のように被加工材の温度が８０
０℃前後あるいはそれより高温のものに対しては、Ｆｅ
基またはＮｉ基のオーステナイト耐熱合金が使用されて
いる。 −
そして、後者のうち巷に安価でかつ高温強度の高い時効
硬化形オーステナイト熱間工具鋼として−は、既に特公
昭５７−１９７４９号に開示されたもの、がある。その
後、前記発明鋼は銅および銅合金押出ダイスとして使用
され、十分な実績を上げている。In addition, the temperature of the workpiece, such as copper and its alloys, is 80°C.
For temperatures around 0°C or higher, Fe
or Ni-based austenitic heat-resistant alloys are used. Among the latter age-hardening austenitic hot work tool steels that are inexpensive and have high high-temperature strength, there is one already disclosed in Japanese Patent Publication No. 19749/1983. Thereafter, the invented steel has been used as copper and copper alloy extrusion dies, and has achieved satisfactory results.
しかし、前記の特公昭５７−１９７４９で開示された時
効硬化形オーステナイト熱間工具鋼は、熱間強度等要求
特性を有し、かつ安価であるが、被剛性が劣るため、複
雑な機械加工を要する工具に適用する場合には、価格的
な利点が発揮されないという問題点があった。However, the age-hardening austenitic hot work tool steel disclosed in the above-mentioned Japanese Patent Publication No. 57-19749 has the required properties such as hot strength and is inexpensive, but has poor rigidity and requires complicated machining. When applied to tools that require this method, there is a problem in that the cost advantage is not achieved.
本発明は、前記特許鋼の高温強度２価格等を保持し、か
つ被剛性を向上せしめた工具鋼を提供することを目的と
する。An object of the present invention is to provide a tool steel that maintains the high-temperature strength and other properties of the patented steel and has improved rigidity.
本発明は、前記の要望に沿って研究した結果、前記特許
鋼（％公昭５７−１９７４９）に５ｔ−０，０３〜０．
３０％およびＺｒ０．２％以下を添加することによシ熱
関強度を大きく損なうことなく、被剛性の問題点を改良
したもので次のような化学組成をもつ。As a result of research in accordance with the above-mentioned demands, the present invention has developed the patented steel (%Koshō 57-19749) with 5t-0.03~0.
By adding 30% and 0.2% or less of Zr, the problem of rigidity was improved without significantly impairing the thermal strength, and it has the following chemical composition.
Ｃ： ０．４１〜１．２ ％ Ｓｔ ： ０．１〜
２．０１Ｍｎ：９．Ｏ〜１４．Ｏ％ Ｃｒ：９．
０〜１７．０％Ｎｉ：１．５〜３．５％ Ｖ：１
．６〜３．６％Ｓ ： ０．０３〜０．３％およびＺｒ
：０．２％以下並びに残部不可避不純物およびＦｅから
なる合金、または前記合金にＷ：０．８〜７．０％１Ｍ
ｏ二０．５〜４．０チのいずれか、またはＷとＭｏを合
計で０．６〜９．５％含有する快削性時効硬化形オース
テナイト工具鋼である。C: 0.41~1.2% St: 0.1~
2.01Mn:9. O~14. O% Cr:9.
0-17.0% Ni: 1.5-3.5% V: 1
．． 6-3.6% S: 0.03-0.3% and Zr
: 0.2% or less and the balance is an alloy consisting of unavoidable impurities and Fe, or the above alloy contains W: 0.8 to 7.0% 1M
It is a free-cutting age-hardening austenitic tool steel containing either 0.5 to 4.0% of O2 or 0.6 to 9.5% of W and Mo in total.
次に本発明鋼の成分限定の理由を述べる。Next, the reason for limiting the composition of the steel of the present invention will be described.
Ｃは鋼のオーステナイト地を強化し、またＶと炭化物を
作ることによって時効硬化を起し、鋼を著しく硬化させ
、かつ耐摩耗性を向上させるために添加するものである
。これ等の効果を十分に発揮させるためには０．４１％
以上が必要であり、多すぎると靭性をそこない時効硬化
性も良くならないので、０．４１〜１．２％に限定する
。C is added to strengthen the austenitic base of the steel and cause age hardening by forming carbides with V, significantly hardening the steel and improving wear resistance. In order to fully demonstrate these effects, 0.41%
The above amount is necessary, and if it is too large, the toughness will be impaired and the age hardenability will not be improved, so it is limited to 0.41 to 1.2%.
Ｓｔは鋼の耐酸化性を増加し、かつ精鋳時の脱酸剤とし
て有効な働きをもつ。０．１％以下では脱酸が不十分と
なシ非金属介在物を増大し、また一方多すぎると−の靭
性および被加工性を損うので、０．１〜２．０チに規定
する。St increases the oxidation resistance of steel and has an effective function as a deoxidizing agent during fine casting. If it is less than 0.1%, deoxidation will be insufficient and nonmetallic inclusions will increase, and if it is too much, the toughness and workability will be impaired, so it is specified as 0.1 to 2.0%. .
Ｍｎは鋼をオーステナイト組織に保持するために添加す
るものである。本発明鋼の優れた高温強度は本発明鋼が
安定したオーステナイト地であることに大きく依存して
いるので庵はきわめて重要な役割を果している。凧は少
なすぎるとオーステナイトが不安定となるので９％以上
が必要であシ、多すぎると耐酸化性をそこなうと同時に
、時効硬化の最高硬さを低下し、高温強度を低下する傾
向があるので、上限を１４％とした。Mn is added to maintain the austenitic structure of the steel. Since the excellent high-temperature strength of the steel of the present invention is largely dependent on the stable austenitic structure of the steel of the present invention, the hermitage plays an extremely important role. If the amount of kite is too small, the austenite will become unstable, so 9% or more is required. If it is too large, it will impair oxidation resistance, reduce the maximum hardness of age hardening, and tend to reduce high-temperature strength. Therefore, the upper limit was set at 14%.
Ｃｒは鋼の耐酸化性を増大し、高温強度を増加させるた
めに添加するものであるが、この効果を十分に発揮する
には９チ以上が望ましく、また１７チを越えると効果少
なく、逆に時効硬化性を低下する傾向がみられるので上
限は１７チとした。Cr is added to increase the oxidation resistance of steel and increase its high-temperature strength, but in order to fully exhibit this effect, it is preferable to use 9 or more Cr, and if it exceeds 17 Cr, the effect is small, and vice versa. The upper limit was set at 17 inches because there is a tendency for the age hardenability to decrease.
■は結晶粒の微細化による靭性の維持及びＶ炭化物の析
出により時効硬化を起し、強度の大きいオーステナイト
にし、耐摩耗性を向上し、さらに高温強度を維持するた
めに添加するものである。(2) is added to maintain toughness by refining the crystal grains, cause age hardening by precipitating V carbides, create strong austenite, improve wear resistance, and maintain high-temperature strength.
１．６％以、下ではこれらの効果が少なく、多すぎると
靭性の低下を生じ、強度向上の効果が飽和するので３．
６チ以下とする。Below 1.6%, these effects will be small, and if it is too much, the toughness will decrease and the strength improvement effect will be saturated, so 3.
Must be 6 inches or less.
Ｎｉの添加は時効硬化性が低下する傾向があるが、靭性
の向上に極めて有効である。Ｎｉ１．５％以下では効果
が少なく、４％以上では時効硬さの低下が顕著となるの
で１．５〜３．５％を請求範囲とした。Although the addition of Ni tends to reduce age hardenability, it is extremely effective in improving toughness. If Ni is less than 1.5%, the effect will be small, and if it is more than 4%, the aging hardness will decrease significantly, so the claimed range is 1.5 to 3.5%.
Ｗは高温強度の増大と耐摩耗性の向上に効果のある元素
である。少なすぎると効果がわずかであシ、多すぎると
効果の上昇が少なく、かつ靭性低下をもたらすので０．
８〜７．０％に限定する。W is an element that is effective in increasing high temperature strength and improving wear resistance. If it is too small, the effect will be slight, and if it is too large, the effect will be little increased and the toughness will decrease, so 0.
Limited to 8-7.0%.
ＭｏもＷと同様の効果を示すがＷよシ時効硬化性に対し
さらに効果が大きく、靭性も低下しがたい。Mo also exhibits the same effects as W, but it has a greater effect on age hardening than W, and the toughness is less likely to decrease.
適当な範囲は０．５〜４チである。Ｗ＋Ｍｏを同時に添
加しても同様な効果が得られる。この場合はＭ。A suitable range is 0.5 to 4 inches. A similar effect can be obtained by adding W+Mo at the same time. In this case M.
が０．５〜４．０％、Ｗが０．８〜７．０ＳＯ範Ｈにお
いてＷとＭｏの合計が０．６〜９．５％添加で高温強度
が十分増加Ｌ、靭性も満足に保たれるのでこのように規
定する。is 0.5 to 4.0% and W is 0.8 to 7.0. In the SO range H, the high temperature strength is sufficiently increased by adding 0.6 to 9.5% of W and Mo in total, and the toughness is also satisfactorily maintained. This is how it is defined.
ＳとＺｒは本発明の特徴をなす元素である。S and Zr are elements that characterize the present invention.
Ｓは被剛性向上のために添加する元素であり、硫化物を
形成するが、少なすぎると効果がわずかであり多すぎる
と靭性の低下を生ずる。このため０．０３〜０．３０％
に規定する。S is an element added to improve stiffness and forms sulfide, but if it is too little, the effect will be slight, and if it is too much, it will cause a decrease in toughness. For this reason, 0.03-0.30%
stipulates.
Ｚｒは被剛性を改善するために添加する元素である。鋼
中にあっては硫化物に対して有効な接種作用を有するＺ
ｒＯ２またはＺｒＮとなる。この接種作用によりて硫化
物の分布の均一化が達成されるので、被剛性改善に役立
つ。多すぎると基地に独立して存在するＺｒ０ｚおよび
ＺｒＮが増大し、かえって被剛性を低下させる危険があ
るので、０．２０％以下の範囲で必要に応じて添加する
。Zr is an element added to improve rigidity. Z has an effective inoculation effect against sulfides in steel.
It becomes rO2 or ZrN. This inoculation effect achieves a uniform distribution of sulfides, which helps improve stiffness. If the amount is too large, Zr0z and ZrN that exist independently in the base will increase, and there is a risk that the rigidity will be lowered. Therefore, it should be added as necessary within a range of 0.20% or less.
以下に本発明の詳細な説明する。 The present invention will be explained in detail below.
第１表に本発明鋼、特許鋼および従来鋼である５ＫＤ５
の実験試料の化学成分を示す。Table 1 shows the invention steel, patented steel, and conventional steel 5KD5.
The chemical composition of the experimental sample is shown below.
ｔａＪ表
第２表は、第１表に示した試料に標準の固溶化処理また
は焼なまし処理を施し、ボール盤でドリルによる切削試
験を行なった結果と試料のかたさを示す。また、実験条
件は、回転数：２７Ｏｒｐｍ。Table 2 of the taJ table shows the results and hardness of the samples obtained by performing a standard solution treatment or annealing treatment on the samples shown in Table 1, and conducting a cutting test using a drill using a drill press. In addition, the experimental conditions were: rotation speed: 27 Orpm.
先端荷重： ８７．５神、ドリル： ５ＫＨ５１，８０
φストレートシヤンクドリル、乾式で数本のドリルを用
い１０■の深さに穿孔するテストである。本表は穿孔の
平均所要時間を指数で比較した。Tip load: 87.5mm, drill: 5KH51,80
This test involves drilling to a depth of 10 mm using a φ straight shank drill and several dry drills. This table compares the average time required for drilling by index.
第 ２ 表
本発明鋼と特許鋼を比較すると、ＳとＺｒの添加により
大幅な被剛性の向上がもたらされ、ＳとＺｒの添加量は
被剛性の改善に対し本発明の成分範囲内では、はぼ比例
的な関係を示すことが判る。Table 2 Comparing the inventive steel and the patented steel, the addition of S and Zr resulted in a significant improvement in stiffness, and the amounts of S and Zr added were within the composition range of the present invention for improving stiffness. , it can be seen that the relationship is almost proportional.
次に第６表に前記の試料について標準の固溶化熱処理温
度または焼入温度から急冷後、表に示す温度で時効また
は焼もどしした時のロックウェルＣかたさを示す。本発
明鋼および特許鋼は１１５０℃に加熱後水冷したものを
時効し、５ＫＤ５は、１０５０℃に加熱後油冷したもの
を焼もどしした。Next, Table 6 shows the Rockwell C hardness of the above samples when they were rapidly cooled from the standard solution heat treatment temperature or quenching temperature and then aged or tempered at the temperatures shown in the table. The invention steel and the patented steel were heated to 1150°C, water-cooled and aged, and 5KD5 was heated to 1050°C, oil-cooled and then tempered.
時効および焼もどしの保持時間は１時間、冷却は急冷で
ある。The holding time for aging and tempering was 1 hour, and the cooling was rapid.
第 ３ 表
本表から次のことが判る。本発明鋼および特許鋼は７５
０℃の時効で最高硬さを示し、それ以上の時効温度でも
かたさ低下は僅少であるが、マルテンサイト鋼である５
ＫＤ５では、６ｏｏ℃以上の焼もどしで急速にかたさを
低下する。その結果、５ＫＤ５は７００℃以上の使用温
度になると強度不足となって、熱へタリ、摩耗などが起
シ工具寿命を減じる。The following can be seen from Table 3. Inventive steel and patented steel are 75
It shows the highest hardness when aged at 0°C, and there is only a slight decrease in hardness even at higher aging temperatures, but it is a martensitic steel.
In KD5, the hardness rapidly decreases when tempered at 60°C or higher. As a result, 5KD5 lacks strength when used at a temperature of 700° C. or higher, leading to thermal deterioration and abrasion, which shortens tool life.
一方、本発明鋼と特許鋼を比較すると、本発明のＳおよ
びＺｒの添加範囲内においては、時効かたさに大きな影
響を与えないことがわかる。On the other hand, when comparing the steel of the present invention and the patented steel, it can be seen that within the addition range of S and Zr of the present invention, aging hardness is not significantly affected.
次に、該試料について高温引張試験を行ない、高温強度
と延性を比較した。その結果を第４表に示す。Next, a high temperature tensile test was conducted on the sample to compare high temperature strength and ductility. The results are shown in Table 4.
第 ４ 表
高温引張試験は平行部径７．０■φ、標点距離２５■の
試験片を第２表で行なったと同じ条件で、固溶化熱処理
または焼入を施し、さらに７５０℃で１時間時効処理ま
たは６００℃で焼もどしを行なった後、８００℃で引張
試験を行なった。Table 4 High-temperature tensile tests were carried out using solution heat treatment or quenching under the same conditions as in Table 2 for test pieces with a parallel part diameter of 7.0 mm and gauge length of 25 mm, and then heated at 750°C for 1 hour. After aging treatment or tempering at 600°C, a tensile test was conducted at 800°C.
８００℃の高温強さは、本発明鋼、特許鋼とも５ＫＤ５
の２倍以上の強さを示す。ＳおよびＺｒの添加の影響は
引張試験においても僅少で、特許鋼の高温強度特性は損
なわれていない。The high temperature strength at 800℃ is 5KD5 for both the invention steel and the patented steel.
It shows more than twice the strength. The effect of the addition of S and Zr was slight even in the tensile test, and the high temperature strength properties of the patented steel were not impaired.
以上述べたように、本発明鋼は従来の熱間ダイス鋼にみ
られない独特の成分配合によシ、特に高温度での使用に
おいて優れた性能を発揮しつつ、常温で被剛性の良好な
時効硬化型オーステナイト系工具鋼である。このため、
耐熱、耐摩耗、耐食性を必要とする各種工具１部品に広
く使用出来るものである０As mentioned above, the steel of the present invention has a unique composition not seen in conventional hot die steels, so it exhibits excellent performance especially when used at high temperatures, and has good stiffness at room temperature. It is an age-hardening austenitic tool steel. For this reason,
Can be widely used for various tool parts that require heat resistance, wear resistance, and corrosion resistance.
Claims (1)
ｎ：９．０〜１４．０％、Ｃｒ：９．０〜１７．０％、
Ｎｉ：１．５〜３．５％、Ｖ：１．６〜３．６％、Ｓ：
０．０３〜０．３およびＺｒ：０．２％以下並びに残部
不可避不純物およびＦｅからなる快削性時効硬化形オー
ステナイト工具鋼。 ２、重量比で Ｃ：０．４１〜１．２％、Ｓｉ：０．１〜２．０％、Ｍ
ｎ：９．０〜１４．０％、Ｃｒ：９．０〜１７．０％、
Ｎｉ：１．５〜３．５％、Ｖ：１．６〜３．６％、Ｓ：
０．０３〜０．３％およびＺｒ：０．２％以下さらにＷ
：０．８〜７．０％およびＭｏ：０．５〜４．０％のい
ずれか、またはＷとＭｏを合計で０．６〜９．５％を含
有し、残部不可避不純物およびＦｅからなる快削性時効
硬化形オーステナイト工具鋼。[Claims] 1. In weight ratio: C: 0.41 to 1.2%, Si: 0.1 to 2.0%, M
n: 9.0-14.0%, Cr: 9.0-17.0%,
Ni: 1.5-3.5%, V: 1.6-3.6%, S:
A free-cutting age-hardening austenitic tool steel comprising 0.03 to 0.3% and Zr: 0.2% or less, and the remainder being unavoidable impurities and Fe. 2. C: 0.41-1.2%, Si: 0.1-2.0%, M in weight ratio
n: 9.0-14.0%, Cr: 9.0-17.0%,
Ni: 1.5-3.5%, V: 1.6-3.6%, S:
0.03 to 0.3% and Zr: 0.2% or less, and W
: 0.8 to 7.0% and Mo: 0.5 to 4.0%, or a total of 0.6 to 9.5% of W and Mo, with the remainder consisting of inevitable impurities and Fe. Free-cutting age-hardening austenitic tool steel.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11818186A JPS62274059A (en) | 1986-05-22 | 1986-05-22 | Free-cutting age-hardening austenitic tool steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11818186A JPS62274059A (en) | 1986-05-22 | 1986-05-22 | Free-cutting age-hardening austenitic tool steel |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS62274059A true JPS62274059A (en) | 1987-11-28 |
Family
ID=14730144
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP11818186A Pending JPS62274059A (en) | 1986-05-22 | 1986-05-22 | Free-cutting age-hardening austenitic tool steel |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS62274059A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1296508C (en) * | 2001-03-05 | 2007-01-24 | 石田清仁 | Free-cutting tool steel |
| CN103526132A (en) * | 2013-09-27 | 2014-01-22 | 泰州永兴合金材料科技有限公司 | Low-nickel stainless steel with high heat resistance and preparation method of stainless steel |
| CN110951947A (en) * | 2019-11-12 | 2020-04-03 | 江阴康瑞成型技术科技有限公司 | Stainless steel bar easy to punch and cut and production process thereof |
-
1986
- 1986-05-22 JP JP11818186A patent/JPS62274059A/en active Pending
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1296508C (en) * | 2001-03-05 | 2007-01-24 | 石田清仁 | Free-cutting tool steel |
| CN103526132A (en) * | 2013-09-27 | 2014-01-22 | 泰州永兴合金材料科技有限公司 | Low-nickel stainless steel with high heat resistance and preparation method of stainless steel |
| CN110951947A (en) * | 2019-11-12 | 2020-04-03 | 江阴康瑞成型技术科技有限公司 | Stainless steel bar easy to punch and cut and production process thereof |
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