JPS59157262A - Low alloy soft nitrided steel - Google Patents
Low alloy soft nitrided steelInfo
- Publication number
- JPS59157262A JPS59157262A JP3103483A JP3103483A JPS59157262A JP S59157262 A JPS59157262 A JP S59157262A JP 3103483 A JP3103483 A JP 3103483A JP 3103483 A JP3103483 A JP 3103483A JP S59157262 A JPS59157262 A JP S59157262A
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- soft
- steel
- nitrided steel
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Abstract
Description
【発明の詳細な説明】
この発明は、軟窒化性にすぐれかつ軟窒化処理後の強度
とくに内部強度が高い低合金軟窒化鋼に関するものであ
る。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a low-alloy soft-nitriding steel that has excellent soft-nitriding properties and high strength, particularly internal strength, after soft-nitriding treatment.
従来、事務機器や自動車などにおいては、機械構造用炭
素鋼や合金鋼などの素材に浸炭処理を施してI耐厚耗性
や疲労強度を向上させた部品が多量に使用されているが
、この浸炭処理には、(1)浸炭焼入時に発生する歪に
よる不良率が高いこと、(2)部品によっては全部品に
対して歪取りのための驕正が必要であり、コスト高とな
りやすいこと、などの欠点がある。Traditionally, in office equipment, automobiles, etc., many parts have been used that are made of materials such as carbon steel and alloy steel for machine structures and have been carburized to improve wear resistance and fatigue strength. Carburizing treatment has two drawbacks: (1) high defect rate due to the distortion that occurs during carburizing and quenching; (2) depending on the part, it may be necessary to straighten all parts to remove distortion, which tends to increase costs. There are drawbacks such as.
一方、このような熱処理歪の大きい浸炭焼入に対し、熱
処理歪の小さい熱処理として、AI変態点以下で表面硬
化処理する窒化処理や軟窒化処理がある。この窒化処理
や軟窒化処理は、被処理材をNH3ガス中に桁いて加熱
し、鋼表面に窒素を浸入させて表面硬度を高める方法で
あるが、従来より一般に使用されている機械構造用炭素
鎖や合金鋼に対して窒化処理または;軟窒化処理を施し
ても十分な硬化層深さを得ることができず、十分な強度
(疲労強度や転勤強度)を#−!Iることかできないと
いう欠点を有していた。このため、従来より種々の軟窒
化鋼が開発されてきたが、それでも強度や軟窒化性が十
分でないという欠点を有していた。On the other hand, in contrast to such carburizing and quenching, which causes large heat treatment distortions, there are nitriding treatments and nitrocarburizing treatments, which are surface hardening treatments below the AI transformation point, as heat treatments with small heat treatment strains. This nitriding treatment and soft nitriding treatment is a method in which the material to be treated is heated in NH3 gas and nitrogen is infiltrated into the steel surface to increase surface hardness. Even if a chain or alloy steel is subjected to nitriding or soft nitriding, a sufficient hardened layer depth cannot be obtained, and sufficient strength (fatigue strength and transfer strength) cannot be obtained. It had the disadvantage of being unable to do much. For this reason, various soft-nitriding steels have been developed, but these still have the disadvantage of insufficient strength and soft-nitriding properties.
この発明は、上述した従来の欠点を解消するためになさ
れたもので、軟窒化性にすぐれ、十分な硬化層深さを得
ることができ、軟窒化処理後の強度とくに内部強度が高
い低合金軟窒化鋼を提供することを目的としている。This invention was made in order to eliminate the above-mentioned conventional drawbacks, and it is a low-alloy alloy that has excellent soft nitriding properties, can obtain a sufficient hardened layer depth, and has high strength, especially internal strength, after soft nitriding. The purpose is to provide soft nitrided steel.
この発明による低合金軟窒化鋼は、C:0.5重量%以
下、Cr:3重量%以下、A文:0.02〜05重量%
を基本成分とし、その他必要に応じて、Ni・3.5重
量%以下、Si:1.5重量%以下、Mn:1.5重量
%以下、Cu:1.5重量%以下、Mo:1.5重量%
以下。The low-alloy soft nitrided steel according to the present invention has C: 0.5% by weight or less, Cr: 3% by weight or less, and A: 0.02-05% by weight.
is the basic component, and if necessary, Ni: 3.5% by weight or less, Si: 1.5% by weight or less, Mn: 1.5% by weight or less, Cu: 1.5% by weight or less, Mo: 1 .5% by weight
below.
W :、 1 、5重量%以下、Co:1.5重量%以
下等のうちの1種または2種以」二を含有する低合金軟
窒化鋼において、V:0.01〜0.5重量%、Ti:
0.01〜0.5ii%、Zr:0.01〜0.5重量
%、Nb+Ta:0.01〜0.5重量%の1種または
2種以」二を含み、S:0.010重量%以下に規制し
たことを特徴とし、また、被削性を改善するために必要
に応じて、Fb:0.01−0.2重量%、Ca:00
005〜001重量%、Se:0.005〜0.1重量
%の1種または2種以上を含有することを特徴とし、よ
り望ましくは0:O,0O20重量%以下に規制したこ
とを特徴としている。そして、この明細書でいう低合金
軟窒化鋼は、部品の素材として使用されることはもちろ
ん、部品や製品そのものであることも当然含まれるもの
である。この場合、前記成分の低合金鋼を所定の部品や
製品形状(例えば、ロール2シャフ1゛、クランクシャ
ツl−、コンロッド、スピンドル、ギヤ、ピン、リーフ
スプリング等)に鍛造。In a low alloy soft nitrided steel containing one or more of the following: W: 1, 5% by weight or less, Co: 1.5% by weight or less, V: 0.01 to 0.5% by weight %, Ti:
Contains one or more of the following: 0.01-0.5ii%, Zr: 0.01-0.5% by weight, Nb+Ta: 0.01-0.5% by weight, S: 0.010% by weight % or less, and if necessary to improve machinability, Fb: 0.01-0.2% by weight, Ca: 00%.
005 to 001% by weight, Se: 0.005 to 0.1% by weight, and more preferably regulated to 0:O, 0O20% by weight or less. There is. The low-alloy soft nitrided steel referred to in this specification naturally includes not only its use as a material for parts, but also the parts and products themselves. In this case, the low alloy steel with the above components is forged into a predetermined part or product shape (for example, roll 2 shaft 1, crank shirt 1, connecting rod, spindle, gear, pin, leaf spring, etc.).
切削、打抜き等の加工により成形し、次いで液体まYこ
は気体もしくはその両名を組み合わせた軟窒化処理を施
し、軟窒化処理後にピンカース硬さくHv)200以上
の内部硬さが得られるようにする。It is formed by cutting, punching, etc., and then subjected to nitrocarburizing using a combination of gas or both to obtain an internal hardness of 200 or higher (Pinker's hardness Hv) after nitrocarburizing. do.
次に、この発明の低合金軟窒化鋼の成分限定理由につい
て説明する。Next, the reason for limiting the composition of the low alloy soft nitrided steel of the present invention will be explained.
C;
Cは鋼の靭性を高めるために必要な元素であり、とくに
内部硬さを増大させて内部強度を高めるのに有効な元素
であるが、多すぎるとかえって靭性を低下し、また加工
性や吸窒化性も劣化させるので、0.5重量%以下とす
る必要があり、特にプレス加工や冷間鍛造加]=する用
途には0.25重子%以下とするのがより望ましい。C; C is an element necessary to increase the toughness of steel, and is particularly effective in increasing internal hardness and increasing internal strength, but if it is in too much, it will actually reduce toughness and reduce workability. Since it also deteriorates nitriding properties, it is necessary to keep it at 0.5% by weight or less, and it is more desirable to keep it at 0.25% by weight or less especially for applications where press working or cold forging is required.
Cr 。Cr.
Crは鋼の軟窒化性を向上するのに寄与する元素であり
、軟窒化処理によって窒化物を形成して表面の硬度を高
めるが、多すぎると軟窒化性向上の効果が飽和すると共
に靭性を劣化させるので、3重量%以下とする必要があ
る。Cr is an element that contributes to improving the soft-nitriding properties of steel, and increases the hardness of the surface by forming nitrides during the soft-nitriding process. However, if too much Cr is present, the effect of improving the soft-nitriding properties becomes saturated and the toughness decreases. Since it causes deterioration, it is necessary to limit the content to 3% by weight or less.
A文 :
Auは鋼の軟窒化性を向上するのに寄与する元素であり
、軟窒化処理によって窒化物を形成して表面の硬度を高
める。そして、このような効果を得るためには0 、0
2fii%以上含有させることが必要であるが、多すぎ
ると鋼の静浄度を低下させると共に靭性を劣化させるの
で、0.5重量%以下とする必要がある。Sentence A: Au is an element that contributes to improving the soft nitriding properties of steel, and forms nitrides through soft nitriding treatment to increase the hardness of the surface. And in order to obtain such an effect, 0,0
It is necessary to contain 2fii% or more, but if it is too large, it reduces the static purity of the steel and deteriorates the toughness, so it is necessary to keep it at 0.5% by weight or less.
Ni、Si、Mn、Cu、Mo、W、Co:Ni、Si
、Mn、Cu、Mo、W、Coは鋼の処理前における強
度を向上し、また、軟窒化処理後の内部強度を一層高め
るのに寄与する元素であるが、多量に添加しても効果の
増大は期硝できず、かえって不経済となるので、上記基
本成分の鋼に添加する場合には、Ni:3.5重量%以
下、Si:1.5重景%以下、Mn:1.5重量%以下
、Cu:1.5重量%以下、 M o :1.5重量%
以下、W: 1.5重量%以下、C。Ni, Si, Mn, Cu, Mo, W, Co: Ni, Si
, Mn, Cu, Mo, W, and Co are elements that contribute to improving the strength of steel before treatment and further increasing the internal strength after soft-nitriding treatment, but even if they are added in large amounts, they are not effective. Since increasing the amount cannot be carried out over time and is rather uneconomical, when adding it to steel with the above basic components, Ni: 3.5% by weight or less, Si: 1.5% by weight or less, Mn: 1.5 Weight % or less, Cu: 1.5 weight % or less, Mo: 1.5 weight %
Hereinafter, W: 1.5% by weight or less, C.
:1.5重量%以下の範囲でこれらの1種または2種以
上を必要に応じて適宜添加するのが良い。: It is preferable to add one or more of these as necessary in an amount of 1.5% by weight or less.
V、Ti、Zr、Nb、Ta:
V、Ti 、Zr、Nb、Taはいずれも軟窒化 ′性
の向上に寄与し、初期の硬度を得るのに必要とする軟窒
化処理時間を短縮するのに有効であると共に、軟窒化処
理後の深部強度を高めるのに有効な元素であるが、多量
に添加しても前記効果の増大は得られず、かえって靭性
を劣化するので、V:0.01〜0.5重量%、Ti
:O,O1〜0.5重量%、Zr:0.01−0.5i
量%。V, Ti, Zr, Nb, Ta: V, Ti, Zr, Nb, and Ta all contribute to improving soft-nitriding properties and shorten the soft-nitriding time required to obtain the initial hardness. V:0. 01-0.5% by weight, Ti
:O, O1-0.5% by weight, Zr: 0.01-0.5i
amount%.
Nb+Ta:0.01〜0.5重湯%ノ範囲テコれらの
1種または2種以上を含有させる。Nb+Ta: 0.01 to 0.5% of heavy hot water contains one or more of these.
S :
S含有量が多すぎると、鋼の軟窒化性を悪化させると共
に、強度とくに内部強度やピッチング強度を低下させる
ので、0.010重塔%以下に規制する。S: If the S content is too large, it deteriorates the soft nitriding properties of the steel and reduces the strength, especially the internal strength and pitting strength, so it is regulated to 0.010% or less.
Pb、Ca’、Se:
Pb、’Ca、Se’は鋼の被削性を向」ニさせるのに
有効な元素であり、S含有量を規制したことによる錆の
被削性低下を補う必要がある場合に添加すると良い。し
かし、多量に添加すると鋼の熱間加工性を害すると共に
、強度および靭性を劣化するので、添加する場合には、
Pb:O,O1〜0.2重子%、Ca:O’、0O05
−0,01重−散%、Se:0.005〜0.1重量%
の範囲でこれらの1種または2種以上を添加するのが良
い。Pb, Ca', Se: Pb, 'Ca, Se' are effective elements for improving the machinability of steel, and are necessary to compensate for the decrease in machinability caused by rust due to regulating the S content. It is good to add it if there is. However, when added in large amounts, it impairs the hot workability of the steel and also deteriorates its strength and toughness, so when adding it,
Pb:O, O1-0.2%, Ca:O', 0O05
-0.01% by weight, Se: 0.005-0.1% by weight
It is preferable to add one or more of these within the following range.
また、0含有量か多すぎると鋼中の介在物量が増加し、
鋼の強度を低下するので、01.0020重Jμ%以下
に規制することがより望ましい。Also, if the content is 0 or too high, the amount of inclusions in the steel will increase,
Since it reduces the strength of the steel, it is more desirable to limit it to 01.0020 Jμ% or less.
このような成分の低合金鋼鋼材あるいは部品等に対して
軟窒化処理を施すことによって、内部硬さがHv200
以上の晶硬度でかつ高強度の軟窒化処理材あるいは軟窒
化処理品(例えは、クランクシャフト、コンロッド、ス
ピンドル、キヤ等)を得ることができる。By applying nitrocarburizing treatment to low-alloy steel materials or parts with such components, the internal hardness can be reduced to Hv200.
It is possible to obtain soft-nitrided materials or soft-nitrided products (for example, crankshafts, connecting rods, spindles, gears, etc.) with crystal hardness above and high strength.
犬施進」
第1表に示す化学成分の鋼を2を電匁炉により溶製した
のち造塊し、次いて直径40mmの丸棒に圧延して、そ
の一部に対してNH3ガス:RXガス−1:1の7囲気
中で580℃X1’、5hr油冷の条件で軟窒化処理を
行って名調の軟窒化性を調r
査し、6部に対しては580°CX 1 、5”N+冷
を施したのちJIS 3号試験片に加工して名調の靭
性値を調査した。その結果を第2表に示す。Steel with the chemical composition shown in Table 1 is melted in an electric furnace, then formed into an ingot, then rolled into a round bar with a diameter of 40 mm, and a part of it is injected with NH3 gas: RX. Soft nitriding was carried out under the conditions of 580°C x 1' and oil cooling for 5 hours in a gas-1:1 atmosphere to investigate the excellent soft nitriding properties, and for 6 parts, 580°C After applying 5"N+cooling, it was processed into a JIS No. 3 test piece and its toughness value was investigated. The results are shown in Table 2.
第 2 表
第1表および第2表に示す結果から明らかなように、本
発明1l(No、1.2,4,6.7)ではいずれも表
面硬さが大であり、Hv550が得られる表層からの距
離(DH,550(mm)) も大きく、内部硬さか大
で内部強度が向上しており、靭性にもすぐれていること
がわかる。これに対してS含有量が多過ぎるN083鋼
では軟窒化性および靭性が劣っており、A交合有量およ
びCr含有に゛か各々多過ぎるNo、 5鋼およびN
o、 7鋼では軟窒化性はすぐれているものの靭性に劣
っていることがわかる。Table 2 As is clear from the results shown in Tables 1 and 2, the surface hardness of the present invention 1l (No. 1.2, 4, 6.7) is high, and Hv550 is obtained. It can be seen that the distance from the surface layer (DH, 550 (mm)) is large, the internal hardness is large, the internal strength is improved, and the toughness is also excellent. On the other hand, steel No. 83, which has too much S content, has poor soft nitriding properties and toughness, and No. 5 steel and N steel have too much A content and Cr content.
It can be seen that steel No. 7 has excellent soft-nitriding properties but is inferior in toughness.
更施例2
第3表に示す化学成分の鋼を2を電気炉により溶製した
のち造塊し、次いで直径40mmの丸棒に圧延して、そ
の一部から回転曲げ疲労試験用の試験片を作製し、各試
験片に対してNH3カス:Rxカス−1:1の雰囲気中
で580°OX1.5hr油冷の条件で軟窒化処理を行
って名調の軟窒化性を調べると共に、小野式回転曲げ疲
労試験(切欠形状係数的1.84)により疲労穢験を行
って名調の疲労強度を調べた。また、前記丸棒の他部に
対して切削試験を行って一部鋼種の被剛性を調へた。な
お、この切削試験では、工4(、: Plo 。Further Example 2 Steel 2 having the chemical composition shown in Table 3 was melted in an electric furnace, then formed into an ingot, and then rolled into a round bar with a diameter of 40 mm, and a portion of the steel was made into a test piece for a rotary bending fatigue test. Each specimen was subjected to nitrocarburizing treatment in an atmosphere of NH3 scum: Rx scum - 1:1 under conditions of oil cooling at 580° A fatigue test was conducted using a rotary bending fatigue test (notch shape factor: 1.84) to examine the fatigue strength of the sample. In addition, cutting tests were conducted on other parts of the round bar to examine the rigidity of some steel types. In addition, in this cutting test, Plo.
送り速度・0 、2mm/rew 、切削深さ+2m
m、切削速度: 150 m/minの条件とした。こ
の結果を第4表に示す。Feed speed: 0, 2mm/rew, cutting depth +2m
m, cutting speed: The conditions were 150 m/min. The results are shown in Table 4.
第4表
第3表および第4表に示す結果から明らかなように、本
発明(No、13〜20)ではいずれも表面硬さが大で
あり、Hv550が得られる表層からの距pa (DH
v 550 (m m ) )も大きく、内部硬さが大
で内部強度が増大しており、疲れ限度も大きいというす
ぐれた特性を示している。そして、この場合Pb、Ca
、Seより選はれる被削性向上元素を添加することによ
って工具寿命を増大させることができ、S含有量の規ル
]による被削性の低下を補うことができた。また、○含
有量が多い場合(NO,18)には疲労強度が低下する
ため、0含イ1量を0.0020重量%に規制すること
がより望ましいこともわかった。これに対してS含有量
が多い比較&’f5 (No、 l 1 、12)て
は被削性は良好であるものの1Iil!:窒化性に劣っ
ており、内部硬さが低く疲労特性も良くないことがわか
った。Table 4 As is clear from the results shown in Tables 3 and 4, the present invention (Nos. 13 to 20) all have high surface hardness, and the distance pa (DH
v 550 (mm)) is large, internal hardness is large, internal strength is increased, and fatigue limit is also large, showing excellent characteristics. In this case, Pb, Ca
By adding a machinability-improving element selected from , Se, the tool life could be increased, and the decrease in machinability caused by the S content rule could be compensated for. It was also found that when the ○ content is large (NO, 18), the fatigue strength decreases, so it is more desirable to limit the 0 content to 0.0020% by weight. On the other hand, the comparison &'f5 (No, l 1, 12) with a high S content has good machinability, but it is 1Iil! : It was found that the nitriding property was poor, the internal hardness was low, and the fatigue properties were also poor.
以上説明してきたように、この発明によれは、軟窒化性
にすぐれ、十分な表面硬度および硬化層深さを得ること
ができ、軟窒化処理後の強度とくに内部強度が高い低合
金軟窒化鋼を得ることができるという非常にすぐれた効
果を有し、1lHtJI耗性および強度が十分良好であ
る鋼素材5部品あるいは製品を得ることがてきる。As explained above, the present invention provides a low-alloy soft-nitrided steel that has excellent soft-nitriding properties, can obtain sufficient surface hardness and hardened layer depth, and has high strength, especially internal strength, after soft-nitriding treatment. It is possible to obtain a steel material 5 parts or product which has a very excellent effect of being able to obtain 11HtJI wear resistance and strength.
特許出願人 大同特殊鋼株式会社 代理人弁理士 小 塩 曲Patent applicant: Daido Steel Co., Ltd. Representative Patent Attorney Shio Koku
Claims (2)
u:0.02〜0.5重量%を基本成分とする低合金軟
窒化鋼において、V:O,O1〜0−5mE’E%、T
i : 0.01〜0.5重fi%。 Zr:0.01〜0.5爪量%爪景N b 十T a
:0.01〜0.5重量%の1種また1走2種以上を含
み、S・0.010重量%以下に規制したことを特徴と
する低合金軟窒化鋼。(1) C: 0.5% by weight or less, Cr: 3% by weight or less, A
In low-alloy soft nitrided steel whose basic component is u: 0.02 to 0.5% by weight, V: O, O1 to 0-5mE'E%, T
i: 0.01 to 0.5 weight fi%. Zr: 0.01~0.5 Nail amount% Nail view N b 10T a
: A low-alloy soft nitrided steel characterized by containing 0.01 to 0.5% by weight of one type or two or more types per run, and regulated to 0.010% by weight or less of S.
下、Al:0.02〜05重量%を基本成分とする低合
金軟窒化鋼において、V:O,O1〜0.5重量%、
T i : 0 、01〜0.5重量%、Zr:0.0
1〜0.5ffi量%、Nb+Ta : 0 、01〜
0 、5重量%の1種または2種以上、およびPb:0
.01〜0.2重量%。 Ca : 0 、0005〜0 、01重要−%、Se
:0 、OQ5〜0.1重置%の1種または2種以上を
含み、S:0.010重量%以下に規制したことを特徴
とする低合金軟窒化鋼。(2) In a low-alloy soft nitrided steel whose basic components are C:' 0.5% by weight or less, Cr: 3% by weight or less, and Al: 0.02-05% by weight, V: O, O1-0.5 weight%,
Ti: 0, 01-0.5% by weight, Zr: 0.0
1~0.5ffi amount%, Nb+Ta: 0, 01~
0, 5% by weight of one or more types, and Pb: 0
.. 01-0.2% by weight. Ca: 0, 0005~0, 01 important-%, Se
A low-alloy soft nitrided steel characterized by containing one or more of the following: 0, OQ: 5 to 0.1% by weight, and S: regulated to 0.010% by weight or less.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP3103483A JPS59157262A (en) | 1983-02-28 | 1983-02-28 | Low alloy soft nitrided steel |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP3103483A JPS59157262A (en) | 1983-02-28 | 1983-02-28 | Low alloy soft nitrided steel |
Publications (1)
Publication Number | Publication Date |
---|---|
JPS59157262A true JPS59157262A (en) | 1984-09-06 |
Family
ID=12320218
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP3103483A Pending JPS59157262A (en) | 1983-02-28 | 1983-02-28 | Low alloy soft nitrided steel |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS59157262A (en) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2002226939A (en) * | 2001-02-01 | 2002-08-14 | Daido Steel Co Ltd | Non-refining steel for soft-nitriding |
JP2006117982A (en) * | 2004-10-20 | 2006-05-11 | Exedy Corp | Method for manufacturing vehicle drive system component |
Citations (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS4924828A (en) * | 1972-06-30 | 1974-03-05 | ||
JPS5118945A (en) * | 1974-08-09 | 1976-02-14 | Daido Steel Co Ltd | TAISHOKUSEINOSUGURETAYOSHOKUKIRUI * HAMONORUINO SEIZOHOHO |
JPS5286920A (en) * | 1976-01-16 | 1977-07-20 | Daido Steel Co Ltd | Soft nitriding low alloy steel |
JPS53149808A (en) * | 1977-05-06 | 1978-12-27 | Hitachi Metals Ltd | Abrasionnresistant steel for nitriding use |
JPS55145155A (en) * | 1979-04-25 | 1980-11-12 | Daido Steel Co Ltd | Suction valve |
JPS55152175A (en) * | 1979-05-18 | 1980-11-27 | Daido Steel Co Ltd | Low-strain high strength gear |
JPS55161055A (en) * | 1979-06-02 | 1980-12-15 | Daido Steel Co Ltd | Low alloy soft-nitriding steel with superior machinability and its product |
JPS55161065A (en) * | 1979-05-22 | 1980-12-15 | Daido Steel Co Ltd | Manufacture of mission synchro mechanism parts having least strain |
JPS5655566A (en) * | 1979-10-06 | 1981-05-16 | Sumitomo Metal Ind Ltd | Production of surface nitrided steel of good toughness |
JPS56119760A (en) * | 1980-02-26 | 1981-09-19 | Daido Steel Co Ltd | Carbonitriding steel |
-
1983
- 1983-02-28 JP JP3103483A patent/JPS59157262A/en active Pending
Patent Citations (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS4924828A (en) * | 1972-06-30 | 1974-03-05 | ||
JPS5118945A (en) * | 1974-08-09 | 1976-02-14 | Daido Steel Co Ltd | TAISHOKUSEINOSUGURETAYOSHOKUKIRUI * HAMONORUINO SEIZOHOHO |
JPS5286920A (en) * | 1976-01-16 | 1977-07-20 | Daido Steel Co Ltd | Soft nitriding low alloy steel |
JPS53149808A (en) * | 1977-05-06 | 1978-12-27 | Hitachi Metals Ltd | Abrasionnresistant steel for nitriding use |
JPS55145155A (en) * | 1979-04-25 | 1980-11-12 | Daido Steel Co Ltd | Suction valve |
JPS55152175A (en) * | 1979-05-18 | 1980-11-27 | Daido Steel Co Ltd | Low-strain high strength gear |
JPS55161065A (en) * | 1979-05-22 | 1980-12-15 | Daido Steel Co Ltd | Manufacture of mission synchro mechanism parts having least strain |
JPS55161055A (en) * | 1979-06-02 | 1980-12-15 | Daido Steel Co Ltd | Low alloy soft-nitriding steel with superior machinability and its product |
JPS5655566A (en) * | 1979-10-06 | 1981-05-16 | Sumitomo Metal Ind Ltd | Production of surface nitrided steel of good toughness |
JPS56119760A (en) * | 1980-02-26 | 1981-09-19 | Daido Steel Co Ltd | Carbonitriding steel |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2002226939A (en) * | 2001-02-01 | 2002-08-14 | Daido Steel Co Ltd | Non-refining steel for soft-nitriding |
JP4556334B2 (en) * | 2001-02-01 | 2010-10-06 | 大同特殊鋼株式会社 | Non-tempered steel hot forged parts for soft nitriding |
JP2006117982A (en) * | 2004-10-20 | 2006-05-11 | Exedy Corp | Method for manufacturing vehicle drive system component |
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