JPH02294463A - Production of nitrified-steel member - Google Patents
Production of nitrified-steel memberInfo
- Publication number
- JPH02294463A JPH02294463A JP11662889A JP11662889A JPH02294463A JP H02294463 A JPH02294463 A JP H02294463A JP 11662889 A JP11662889 A JP 11662889A JP 11662889 A JP11662889 A JP 11662889A JP H02294463 A JPH02294463 A JP H02294463A
- Authority
- JP
- Japan
- Prior art keywords
- nitriding
- steel member
- ion
- treatment
- nitriding treatment
- 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
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 49
- 239000010959 steel Substances 0.000 title claims abstract description 49
- 238000004519 manufacturing process Methods 0.000 title claims description 13
- 238000005121 nitriding Methods 0.000 claims abstract description 103
- 238000011282 treatment Methods 0.000 claims abstract description 69
- 238000000034 method Methods 0.000 claims abstract description 13
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 abstract description 38
- 229910052757 nitrogen Inorganic materials 0.000 abstract description 19
- 238000009792 diffusion process Methods 0.000 abstract description 15
- 239000010410 layer Substances 0.000 abstract description 14
- 150000004767 nitrides Chemical class 0.000 abstract description 12
- 239000002344 surface layer Substances 0.000 abstract description 11
- 150000002500 ions Chemical class 0.000 description 24
- 230000007423 decrease Effects 0.000 description 6
- 239000007789 gas Substances 0.000 description 6
- 239000000463 material Substances 0.000 description 6
- 238000010586 diagram Methods 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 230000035515 penetration Effects 0.000 description 4
- 230000003247 decreasing effect Effects 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 229910001337 iron nitride Inorganic materials 0.000 description 3
- 229910000851 Alloy steel Inorganic materials 0.000 description 2
- 229910000727 Fe4N Inorganic materials 0.000 description 2
- 238000005452 bending Methods 0.000 description 2
- 238000009661 fatigue test Methods 0.000 description 2
- 125000004433 nitrogen atom Chemical group N* 0.000 description 2
- 238000010606 normalization Methods 0.000 description 2
- 150000003839 salts Chemical class 0.000 description 2
- 229920006395 saturated elastomer Polymers 0.000 description 2
- 238000005496 tempering Methods 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- TZCXTZWJZNENPQ-UHFFFAOYSA-L barium sulfate Chemical compound [Ba+2].[O-]S([O-])(=O)=O TZCXTZWJZNENPQ-UHFFFAOYSA-L 0.000 description 1
- 229910052601 baryte Inorganic materials 0.000 description 1
- 239000010428 baryte Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000000903 blocking effect Effects 0.000 description 1
- 238000005255 carburizing Methods 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 229910000859 α-Fe Inorganic materials 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〕
本発明は窒化鋼部材の製造方法に関し、特にイオン窒化
又はイオン軟窒化の窒化処理を温度を変えて２工程で施
し有効硬化深さ及び表面硬さを著しく改善し得る方法に
関するものである。[Detailed Description of the Invention] [Field of Industrial Application] The present invention relates to a method for manufacturing nitrided steel members, and in particular, the nitriding treatment of ion nitriding or ion soft nitriding is performed in two steps at different temperatures to improve the effective hardening depth and surface. The present invention relates to a method that can significantly improve hardness.
従来、鋼部材を用いて疲労強度に優れる歯車などの鋼部
材を製造する技術として、鋼部材に浸炭処理を施す技術
と、鋼部材に窒化処理や軟窒化処理を施す技術が広く実
用化されている。Conventionally, as a technology for manufacturing steel parts such as gears with excellent fatigue strength using steel parts, the technology of carburizing the steel parts and the technology of applying nitriding or nitrocarburizing to the steel parts have been widely put into practical use. There is.
上記窒化処理や軟窒化処理は約５００〜６００℃程度の
低温で処理する関係上熱処理歪が僅少であり精密機械部
品に適用するのに適しているが、硬化層が浅いことから
疲労強度向上の面で改善の余地が残されている。The above-mentioned nitriding and soft-nitriding treatments are performed at a low temperature of about 500 to 600°C, so the heat treatment distortion is small, so they are suitable for application to precision mechanical parts, but because the hardened layer is shallow, it is difficult to improve fatigue strength. There is still room for improvement in this respect.
上記窒化処理や軟窒化処理を施すと、鋼部材の表層に窒
化鉄（Ｆｅ２Ｎ−．Ｆｅ＝Ｎ，Ｆｅ４Ｎ）からなる憂硬
度の窒化物被膜が形成され、同時に鋼部材の内部にも窒
化物（拡散硬化層）が形成され、疲労寿命が著しく向上
する。When the above-mentioned nitriding treatment or soft nitriding treatment is performed, a hard nitride film consisting of iron nitride (Fe2N-.Fe=N, Fe4N) is formed on the surface layer of the steel member, and at the same time, nitride ( diffusion hardening layer) is formed, significantly improving fatigue life.
上記表層の窒化物被膜の内側の拡散硬化層を極力深く形
成することが重要であるとの観点から、窒化処理に際し
綱組織を最適化し、表面近傍の金属組織をフエライト＋
バーライト組織にすることも提案されている（特公昭６
１−３１１８４号公報参照）。From the viewpoint that it is important to form the diffusion hardened layer inside the surface nitride coating as deep as possible, we optimized the steel structure during the nitriding process and changed the metal structure near the surface to ferrite +
It has also been proposed to make it a barite organization (Special Public Relations Act
1-31184).
一方、通常、軟窒化用の合金鋼部材に窒化処理や軟窒化
処理を施した場合、第１図の曲線Ａに示すようにＨＶ５
００となる有効硬化深さは０．１ｆｌ程度また表面硬さ
はＨｖ６５０程度である。上記有効硬化深さ及び表面硬
さを改善する為、一般に採用される対策は、窒化処理温
度を高くし且つ処理時間を長くすることである。On the other hand, when an alloy steel member for nitrocarburizing is subjected to nitriding treatment or nitrocarburizing treatment, the HV5
The effective hardening depth of 0.00 is about 0.1 fl and the surface hardness is about Hv650. In order to improve the effective hardening depth and surface hardness, a commonly adopted measure is to increase the nitriding temperature and lengthen the treatment time.
上記のように窒化処理温度を高め、処理時間を長くした
場合に、次のような種々の問題が生じる．＋１１ 窒
化処理温度を高くすると泪部材中の基材の焼戻し作用が
大となり、基材の硬さが低下してしまう。また、窒化物
の生成が不十分となり窒化層の硬さが低下する。When the nitriding temperature is increased and the treatment time is increased as described above, the following various problems occur. +11 When the nitriding temperature is increased, the tempering effect of the base material in the tear member increases, and the hardness of the base material decreases. Furthermore, the hardness of the nitride layer decreases due to insufficient formation of nitrides.
（２） −３１に採用されるガス軟窒化や塩浴窒化の
場合、処理時間を長くしても、有効硬化深さが略一定値
（０．２〜０．３ｍｍ）で飽和する。これは、鋼部材の
表面に形成される窒化鉄化合物層（ＦｅｚＮ、ＦｅｚＮ
，Ｆｅ４Ｎ）が時間経過とともに成長して厚くなり、窒
素の侵入が遮断されるためであると考えられる。(2) In the case of gas soft nitriding or salt bath nitriding employed in -31, the effective hardening depth saturates at a substantially constant value (0.2 to 0.3 mm) even if the treatment time is increased. This is an iron nitride compound layer (FezN, FezN) formed on the surface of a steel member.
, Fe4N) grows and becomes thicker over time, blocking the intrusion of nitrogen.
そこで、本発明の発明者は、窒素の侵入力に優れるイオ
ン窒化処理を採用し、その処理時間を長くして実験した
結果、Ｈｖ５００となる有効硬化深さ０． ３ ｍを実
現することが出来たけれども、第１図の曲線Ｂに示すよ
うに表面硬さが低下してしまうという問題が生じた。鋼
部材の表面硬さは強度及び疲労強度及び耐摩耗性等に大
きく影響することから、表面硬さを向上させることが必
要である。Therefore, the inventors of the present invention adopted ion nitriding treatment which has excellent nitrogen penetration power, and as a result of experimenting by increasing the treatment time, they found that the effective hardening depth was 0.5 mm, which resulted in Hv500. 3 m was achieved, but a problem arose in that the surface hardness decreased, as shown by curve B in Figure 1. Since the surface hardness of a steel member greatly affects its strength, fatigue strength, wear resistance, etc., it is necessary to improve the surface hardness.
本発明の目的は、有効硬化深さ約０． ３ ａｓ以上及
び表面硬さＨｖ７００以上となるような窒化鋼部材の製
造方法を提供することである。It is an object of the present invention to have an effective hardening depth of about 0. It is an object of the present invention to provide a method for manufacturing a nitrided steel member having a hardness of 3 as or more and a surface hardness of Hv700 or more.
本発明に係る窒化鋼部材の製造方法は、鋼部材に窒化処
理を施して窒化鋼部材を製造する窒化鋼部材の製造方法
において、鋼部材に、５５０〜６００℃の温度で５〜１
５時間の間イオン窒化又はイオン軟窒化による第１窒化
処理を施し、次に上記鋼部材に、４５０〜５３０℃の温
度で０． ５〜３時間の間イオン窒化又はイオン軟窒化
による第２窒化処理を施すものである。The method for manufacturing a nitrided steel member according to the present invention is a method for manufacturing a nitrided steel member in which the steel member is subjected to a nitriding treatment to produce a nitrided steel member.
A first nitriding treatment by ion nitriding or ion soft nitriding was performed for 5 hours, and then the steel member was subjected to a 0. A second nitriding treatment is performed by ion nitriding or ion soft nitriding for 5 to 3 hours.
本発明に係る窒化鋼部材の製造方法においては、第２図
又は第３図に示すように、鋼部材に、５５０〜６００℃
の温度で５〜１５時間の間イオン窒化又はイオン軟窒化
による第１窒化処理を施し、次に上記鋼部材に４５０〜
５３０℃の温度で０． ５〜３時間の間イオン窒化又は
イオン軟窒化による第２窒化処理を施す。In the method for manufacturing a nitrided steel member according to the present invention, as shown in FIG. 2 or 3, the steel member is heated to 550 to 600°C.
The steel member is then subjected to a first nitriding treatment by ion nitriding or ion soft nitriding at a temperature of 450 to 15 hours.
0.0 at a temperature of 530°C. A second nitriding treatment using ion nitriding or ion soft nitriding is performed for 5 to 3 hours.
先ず、第１窒化処理について説明すると、イオン窒化や
イオン軟窒化はイオンの侵入力が強力なので窒化による
拡散硬化層が深くまで形成され易く、５５０〜６００℃
の比較的高い温度まで鋼部材を加熱して窒化処理するの
でまた５〜１５時間の比較的長時間の間窒化処理するの
で、窒化による拡散硬化層が深くまで形成されることに
なる。First, to explain the first nitriding treatment, ion nitriding and ion soft nitriding have a strong ion penetration force, so it is easy to form a deep diffusion hardened layer due to nitriding.
Since the nitriding treatment is performed by heating the steel member to a relatively high temperature of , and the nitriding treatment is performed for a relatively long time of 5 to 15 hours, a diffusion hardened layer due to nitridation is formed deep.
第１窒化処理をイオン窒化又はイオン軟窒化により行な
うのは、ガス軟窒化や塩浴窒化では窒素原子の鋼部材中
への十分な侵入力が得られないからである。The reason why the first nitriding treatment is performed by ion nitriding or ion soft nitriding is that gas soft nitriding or salt bath nitriding cannot provide sufficient penetration force of nitrogen atoms into the steel member.
処理温度を５５０〜６００℃とするのは、５００℃未満
では深い拡散硬化層を形成するのに長時間を要し実用性
に欠けること、また６００℃より高いと窒化物が析出し
に＜＜シかも鋼基材の焼戻し作用が過大となって鋼基材
の硬さが低下してしまうこと、などの理由によるもので
ある。The reason why the treatment temperature is set at 550 to 600°C is that if it is less than 500°C, it will take a long time to form a deep diffusion hardened layer, which is impractical, and if it is higher than 600°C, nitrides will precipitate. This is probably due to the fact that the tempering action of the steel base material becomes excessive and the hardness of the steel base material decreases.
処理時間を５〜１５時間とするのは、５時間未満では拡
散硬化層を余り深くまで形成できないこと、１５時間よ
り長くしても処理時間長期化の効果が飽和してしまうこ
と、などの理由によるものである．
ところで、上記第１窒化処理のみでは、有効硬化深さは
０． ３ ｗ以上となるが、表面硬さがＨｖ７００未満
になってしまう。The reason why the treatment time is set to 5 to 15 hours is that if it is less than 5 hours, the diffusion hardened layer cannot be formed very deeply, and if it is longer than 15 hours, the effect of prolonging the treatment time will be saturated. This is due to By the way, with only the first nitriding treatment, the effective hardening depth is 0. 3 W or more, but the surface hardness becomes less than Hv700.
その理由について考察してみると、処理温度を高め処理
時間を長くすると、窒素原子の鋼部材内部への拡散は進
行し、これと並行して鋼部材の表面の窒化鉄などの窒化
物層が厚くなってい《。その結果、窒化物層により窒素
の侵入が妨げられ窒素の侵入量が減少していって、ある
時点において窒素の侵入量が内部への拡散量よりも少な
くなり、これにより表面層の窒素量が不足して表面層の
硬さが内部よりも低下するものと考えられる。When we consider the reason for this, when we raise the processing temperature and lengthen the processing time, the diffusion of nitrogen atoms into the steel parts progresses, and at the same time, the nitride layer such as iron nitride on the surface of the steel parts progresses. It's getting thicker《. As a result, the nitride layer prevents nitrogen from entering and the amount of nitrogen entering decreases.At a certain point, the amount of nitrogen entering becomes less than the amount of diffusion into the interior, which causes the amount of nitrogen in the surface layer to decrease. It is thought that the hardness of the surface layer is lower than that of the inside due to insufficient hardness.
上記のように窒素量が不足した表面層へ窒素を補充する
為、本発明特有の第２窒化処理を施すのである。In order to replenish nitrogen to the surface layer where the amount of nitrogen is insufficient as described above, the second nitriding treatment unique to the present invention is performed.
この第２窒化処理を第１窒化処理よりも低い温度（４５
０〜５３０℃）で行なうので、窒素の鋼部材の内部への
拡散力が第１窒化処理のときの拡散力よりも弱くなり、
侵入窒素の大部分は表面層に留まって窒化物を形成し、
第１図の曲線Ｃに示すように表面層の硬さが大幅に向上
する。This second nitriding treatment is carried out at a temperature lower than that of the first nitriding treatment (45
0 to 530°C), the diffusion force of nitrogen into the interior of the steel member is weaker than that during the first nitriding treatment,
Most of the invading nitrogen remains in the surface layer and forms nitrides,
As shown by curve C in FIG. 1, the hardness of the surface layer is significantly improved.
第２窒化処理をイオン窒化又はイオン軟窒化により行な
うのは、第１窒化処理の場合と同じ理由による。The second nitriding process is performed by ion nitriding or ion soft nitriding for the same reason as the first nitriding process.
処理温度を４５０〜５３０℃とするのは、４５０℃未満
では窒化反応が有効に進行しないこと、また５３０℃よ
り高《なると鋼部材の内部への窒素の拡散が促進されて
表面層に窒素を留めることができないこと、などの理由
によるものである。The reason why the treatment temperature is set at 450 to 530°C is because the nitriding reaction does not proceed effectively below 450°C, and when it is higher than 530°C, the diffusion of nitrogen into the interior of the steel member is promoted and nitrogen is deposited in the surface layer. This is due to reasons such as the inability to keep it in place.
処理時間を０．５〜３時間とするのは、０．５時間未満
では十分な窒化反応が得られないこと、また３時間より
長くしてもその効果が飽和してしまうこと、などの理由
によるものである。The reason why the treatment time is set to 0.5 to 3 hours is that a sufficient nitriding reaction cannot be obtained if the treatment time is less than 0.5 hours, and the effect is saturated if the treatment time is longer than 3 hours. This is due to
上記第２窒化処理を施すことにより、鋼部材の表面層に
窒素を補充して十分な窒化物を形成することが出来、表
面層の硬さをＨＶ７００以上まで高めることが出来る。By performing the second nitriding treatment, the surface layer of the steel member can be supplemented with nitrogen to form sufficient nitrides, and the hardness of the surface layer can be increased to HV700 or higher.
尚、第２図に示すように第１窒化処理に引き続いて第２
窒化処理を施してもよいし、或いは第３図に示すように
第１窒化処理後鋼部材の温度が十分低下してから且つ必
要に応じて任意の時間経過後に第２窒化処理を施しても
よい。Furthermore, as shown in Fig. 2, the second nitriding treatment is carried out following the first nitriding treatment.
The nitriding treatment may be performed, or the second nitriding treatment may be performed after the temperature of the steel member has sufficiently decreased after the first nitriding treatment and after an arbitrary period of time has elapsed as necessary, as shown in Fig. 3. good.
尚、本発明は鋼全般に亙って適用し得るが、特に窒化物
を形成しやすい元素（Ｃｒ、■、Ａ１、Ｔｉなど）を適
量含有する合金鋼が望ましい６〔発明の効果〕
本発明に係る窒化鋼部材の製造方法によれば、上記〔作
用〕の項で詳述したように、第１窒化処理と第２窒化処
理とを施すことにより、窒化鋼部材の有効硬化深さが０
． ３ ｗ以上まで大きくなり、且つ表面硬さがＨＶ７
００以上まで高くなることから、特に疲労強度と耐摩耗
性に優れた窒化鋼部材を製造することが出来る。Although the present invention can be applied to steels in general, alloy steels containing appropriate amounts of elements that easily form nitrides (Cr, ■, A1, Ti, etc.) are particularly desirable6 [Effects of the Invention] The present invention According to the method for manufacturing a nitrided steel member, as detailed in the [Operation] section above, by performing the first nitriding treatment and the second nitriding treatment, the effective hardening depth of the nitrided steel member is reduced to 0.
．． 3W or more, and the surface hardness is HV7.
00 or higher, it is possible to manufacture nitrided steel members with particularly excellent fatigue strength and wear resistance.
以下、本発明の実施例について図面を参照し乍ら説明す
る。Embodiments of the present invention will be described below with reference to the drawings.
第４図に示すように、下記の第１表の組成の合金鋼の畑
材を所定サイズに切断し、その鋼材に熱間鍛造を施して
２０ｗφの丸棒を多数製作し、それら丸棒を９００℃ま
で加熱して焼準を施した。As shown in Fig. 4, we cut the field materials of alloy steel with the composition shown in Table 1 below into a predetermined size, hot forged the steel material to produce a large number of 20wφ round bars, and then It was heated to 900°C and normalized.
それら焼準後の丸棒の表面部の硬さはＨｖ２７０であっ
た。The surface hardness of the round bars after normalization was Hv270.
次に、それら丸捧を機械加工し、第５図のような回転曲
げ疲労試験片Ｐを製作した。Next, these round pieces were machined to produce rotating bending fatigue test pieces P as shown in FIG.
（本頁以下余白）
第１表
〔単位：重量％〕
次に、上記多数の試験片の夫々に対して第２表に示すよ
うに第１窒化処理を施し、次に第２窒化処理を施した。(Margin below this page) Table 1 [Unit: Weight %] Next, each of the above-mentioned large number of test pieces was subjected to the first nitriding treatment as shown in Table 2, and then the second nitriding treatment was performed. did.
尚、第１窒化処理と第２窒化処理には同種の窒化処理を
施し、比較例の試験Ｎｏ． １及び４のものには第２窒
化処理を施していない。Note that the same type of nitriding treatment was performed for the first nitriding treatment and the second nitriding treatment, and test No. 1 of the comparative example was used. Nos. 1 and 4 were not subjected to the second nitriding treatment.
但し、ガス軟窒化処理にはＮＨ．：ＲＸ（吸熱型変成ガ
ス）＝１：１のガスを用い、イオン窒化処理にはＮｚ
：Ｈ２ ＝１ ： １のガスを用いた。However, NH. :RX (endothermic metamorphic gas) = 1:1 gas is used, and Nz is used for ion nitriding treatment.
:H2=1:1 gas was used.
次に、上記のように窒化処理を施した試験片の夫々につ
いて表面下５０μｍ位置の断面硬さの測定及びビソカー
ス硬さＨｖ５００以上の有効硬化深さを測定した。Next, for each of the test pieces subjected to the nitriding treatment as described above, the cross-sectional hardness at a position of 50 μm below the surface and the effective hardening depth at a viscous hardness of Hv500 or more were measured.
更に、上記の測定と並行して、各試験片と同一条件で製
作した試験片について５０ｋｇｆ／１ｍ”の試験応力に
て回転曲げ疲労試験を実施し、破損するまでの負荷サイ
クル数を疲労寿命とした（第２表参照）。In addition, in parallel with the above measurements, a rotating bending fatigue test was conducted on test pieces manufactured under the same conditions as each test piece at a test stress of 50 kgf/1 m'', and the number of load cycles until failure was determined as the fatigue life. (See Table 2).
（本頁以下余白） 次に、第２表の内容について説明する。(Margins below this page) Next, the contents of Table 2 will be explained.
ｍｌ及び患２では、ガス軟窒化を施したので、窒素の侵
入力が低いため十分な拡散硬化層が得られない。In cases ml and 2, gas nitrocarburizing was performed, so a sufficient diffusion hardened layer could not be obtained because the nitrogen penetration force was low.
１１ｈ３では、イオン窒化による第１窒化処理の処理時
間が短かいので十分な拡散硬化層が得られないが、第２
窒化処理を施したので断面硬さが向上している。In 11h3, the treatment time of the first nitriding treatment using ion nitriding is short, so a sufficient diffusion hardened layer cannot be obtained.
The nitriding treatment improves cross-sectional hardness.
患４では、イオン窒化による第１窒化処理の処理時間を
十分長くしたので有効硬化深さが著しく向上しているけ
れども、第２窒化処理を施さないので表面付近の窒素量
が不足し断面硬さが改善されていない。In Case 4, the treatment time of the first nitriding treatment using ion nitriding was made sufficiently long, so the effective hardening depth was significantly improved, but since the second nitriding treatment was not performed, the amount of nitrogen near the surface was insufficient and the cross-sectional hardness decreased. has not been improved.
患５では、イオン窒化処理による第１及び第２窒化処理
を施したが、第２窒化処理の温度が高すぎるので内部へ
の窒素の拡散により表面付近の窒素量が不足した結果断
面硬さが改善されない。In case No. 5, the first and second nitriding treatments using ion nitriding were performed, but since the temperature of the second nitriding was too high, the amount of nitrogen near the surface was insufficient due to the diffusion of nitrogen into the interior, resulting in a decrease in cross-sectional hardness. No improvement.
阻６では、イオン窒化による第１及び第２窒化処理を施
したが、第２窒化処理の温度が低いため表面付近におけ
る窒化反応が不十分となり断面硬さが殆んど改善されな
い。In case No. 6, first and second nitriding treatments using ion nitriding were performed, but since the temperature of the second nitriding treatment was low, the nitriding reaction near the surface was insufficient and the cross-sectional hardness was hardly improved.
Ｎ１１７、隘８及びＩｌｉｌ９のものは、イオン窒化に
よる第１及び第２窒化処理の温度と処理時間とを夫々適
切に設定したので、０．３４ｍｍ以上もの有効硬化深さ
及びＨｖ７５０以上もの断面硬さとなっている。その理
由は、〔作用〕の項に記載した通りであるので省略する
。For N117, No. 8, and Ilil 9, the temperature and treatment time of the first and second nitriding treatments using ion nitriding were appropriately set, respectively, resulting in an effective hardening depth of 0.34 mm or more and a cross-sectional hardness of Hv 750 or more. It has become. The reason for this is the same as described in the [Operation] section, so it will be omitted.
尚、実用に供する窒化鋼部材を製造する際には、前記焼
準処理は省略してもよいし、また第４図に示すように必
要に応じて第２窒化処理を施してから窒化鋼部材にショ
ットビーニング処理を施して疲労強度の向上を図ること
も有る。In addition, when manufacturing nitrided steel members for practical use, the normalization treatment may be omitted, or, as shown in FIG. Shot beaning may also be applied to improve fatigue strength.
第１図は従来技術と本発明に係る窒化鋼部材の硬さの特
性図、第２図及び第３図は夫々本発明における窒化処理
の熱処理サイクルの説明図、第４図は実施例に係る窒化
鋼部材の製造工程説明図、第５図は実施例に係る試験片
の説明図である。Fig. 1 is a characteristic diagram of the hardness of nitrided steel members according to the prior art and the present invention, Figs. 2 and 3 are explanatory diagrams of the heat treatment cycle of nitriding treatment in the present invention, respectively, and Fig. 4 is a diagram according to an example. FIG. 5 is an explanatory diagram of a manufacturing process of a nitrided steel member, and FIG. 5 is an explanatory diagram of a test piece according to an example.
Claims (1)
窒化鋼部材の製造方法において、鋼部材に、５５０〜６
００℃の温度で５〜１５時間の間イオン窒化又はイオン
軟窒化による第１窒化処理を施し、 次に上記鋼部材に、４５０〜５３０℃の温度で０．５〜
３時間の間イオン窒化又はイオン軟窒化による第２窒化
処理を施すことを特徴とする窒化鋼部材の製造方法。(1) In a method for manufacturing a nitrided steel member, in which the steel member is subjected to nitriding treatment to produce a nitrided steel member, the steel member is
A first nitriding treatment using ion nitriding or ion soft nitriding is performed at a temperature of 0.00°C for 5 to 15 hours, and then the steel member is subjected to a nitriding treatment of 0.5 to
A method for manufacturing a nitrided steel member, comprising performing a second nitriding treatment by ion nitriding or ion soft nitriding for 3 hours.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11662889A JPH02294463A (en) | 1989-05-10 | 1989-05-10 | Production of nitrified-steel member |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11662889A JPH02294463A (en) | 1989-05-10 | 1989-05-10 | Production of nitrified-steel member |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH02294463A true JPH02294463A (en) | 1990-12-05 |
Family
ID=14691905
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP11662889A Pending JPH02294463A (en) | 1989-05-10 | 1989-05-10 | Production of nitrified-steel member |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH02294463A (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03204479A (en) * | 1989-12-29 | 1991-09-06 | Nippon Piston Ring Co Ltd | Piston ring and its manufacture |
| US5176760A (en) * | 1991-11-22 | 1993-01-05 | Albert Young | Steel article and method |
| JP2006077315A (en) * | 2004-09-13 | 2006-03-23 | Juki Corp | Thread cutter of sewing machine |
| JP2006216443A (en) * | 2005-02-04 | 2006-08-17 | Hitachi Ltd | Metal sheath magnesium diboride superconducting wire rod and its manufacturing method |
| JP2007056368A (en) * | 2005-07-29 | 2007-03-08 | Showa Denko Kk | Surface treatment method for aluminum extruding die, and aluminum extruding die |
-
1989
- 1989-05-10 JP JP11662889A patent/JPH02294463A/en active Pending
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03204479A (en) * | 1989-12-29 | 1991-09-06 | Nippon Piston Ring Co Ltd | Piston ring and its manufacture |
| US5176760A (en) * | 1991-11-22 | 1993-01-05 | Albert Young | Steel article and method |
| JP2006077315A (en) * | 2004-09-13 | 2006-03-23 | Juki Corp | Thread cutter of sewing machine |
| JP4546793B2 (en) * | 2004-09-13 | 2010-09-15 | Ｊｕｋｉ株式会社 | Sewing machine thread trimming device |
| JP2006216443A (en) * | 2005-02-04 | 2006-08-17 | Hitachi Ltd | Metal sheath magnesium diboride superconducting wire rod and its manufacturing method |
| JP2007056368A (en) * | 2005-07-29 | 2007-03-08 | Showa Denko Kk | Surface treatment method for aluminum extruding die, and aluminum extruding die |
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