JPH1150141A - Surface hardening treatment for steel parts - Google Patents
Surface hardening treatment for steel partsInfo
- Publication number
- JPH1150141A JPH1150141A JP21984397A JP21984397A JPH1150141A JP H1150141 A JPH1150141 A JP H1150141A JP 21984397 A JP21984397 A JP 21984397A JP 21984397 A JP21984397 A JP 21984397A JP H1150141 A JPH1150141 A JP H1150141A
- Authority
- JP
- Japan
- Prior art keywords
- treatment
- gas
- temperature
- test
- steel parts
- 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.)
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- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、鋼製部品を表面硬
化処理する方法、特にガス軟窒化処理を含む表面硬化処
理方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method of surface hardening steel parts, and more particularly to a method of surface hardening including gas nitrocarburizing.
【０００２】[0002]
【従来の技術】ガス軟窒化処理は、浸炭窒化性のガス雰
囲気で、５９０℃未満、標準的には５７０〜５８０℃で
熱処理して、表面に硬質の鉄−窒素化合物層と窒素の拡
散層とを形成する表面硬化処理法で、この処理を施した
鋼製部品は、耐摩耗性および耐食性に著しく優れたもの
となる。2. Description of the Related Art A gas nitrocarburizing treatment is performed in a carbonitriding gas atmosphere at a temperature of less than 590 ° C., typically at 570 to 580 ° C., to form a hard iron-nitrogen compound layer and a nitrogen diffusion layer on the surface. The steel part subjected to this treatment by the surface hardening method, which has the following characteristics, has remarkably excellent wear resistance and corrosion resistance.
【０００３】[0003]
【発明が解決しようとする課題】しかしながら、ガス軟
窒化処理を施した鋼製部品が、比較的炭素含有量の低い
炭素鋼（例えば、ＪＩＳ Ｓ２５Ｃなど）からなるよう
な場合は、耐摩耗性が十分であるにもかかわらず打痕傷
が付き易く、例えば、油圧緩衝器やガススプリングのピ
ストンロッドなどでは、この打痕傷が寿命決定要因とな
り、早期に寿命に達するという問題を生ずることがあっ
た。However, when the steel part subjected to the gas nitrocarburizing treatment is made of carbon steel having a relatively low carbon content (for example, JIS S25C, etc.), the wear resistance is reduced. In spite of being sufficient, dents are likely to be formed. Was.
【０００４】なお、上記した打痕傷は、ガス軟窒化処理
により形成される表面の鉄−窒素化合物層が、せいぜい
２０μｍ程度の厚さであり、その下に窒素の拡散層が相
当の厚さ（０．３〜０．５ｍｍ程度）で存在するとはい
え、その拡散層の硬さが不十分であることによると推定
される。In the above-mentioned dent scar, the iron-nitrogen compound layer on the surface formed by the gas nitrocarburizing treatment has a thickness of at most about 20 μm, and a nitrogen diffusion layer underneath has a considerable thickness. (About 0.3 to 0.5 mm), it is presumed that the hardness of the diffusion layer is insufficient.
【０００５】本発明は、上記従来の問題点に鑑みてなさ
れたもので、その目的とするところは、耐摩耗性および
耐食性の向上に効果的なガス軟窒化処理の特性を生かし
つつ、打痕に対する抵抗性の向上にも寄与する鋼製部品
の表面硬化処理方法を提供することにある。The present invention has been made in view of the above-mentioned conventional problems, and an object of the present invention is to obtain a dent while utilizing the characteristics of a gas nitrocarburizing treatment which is effective in improving abrasion resistance and corrosion resistance. An object of the present invention is to provide a method for surface hardening a steel part which also contributes to an improvement in resistance to steel.
【０００６】[0006]
【０００７】本発明は、上記目的を達成するため、鋼製
部品を５９０℃未満の温度でガス軟窒化処理した後、該
鋼製部品を５９０℃以上でかつその鋼に特有のＡ1 変態
点未満の温度範囲に加熱し、続いて急冷するようにした
ことを特徴とする。[0007] The present invention, in order to achieve the above object, after processing gas soft steel parts at a temperature below 590 ° C., and the steel parts made of 590 ° C. or higher 1 transformation point of the specific A on the steel It is characterized in that it is heated to a temperature range below, and then rapidly cooled.
【０００８】一般に、鋼製部品にガス軟窒化処理を施す
と、最表面に鉄−窒素化合物層が形成されると共に、そ
の化合物層下に窒素の拡散層が形成される。この場合、
前記鉄−窒素化合物層の窒素含有量は８〜１０wt％、拡
散層の窒素含有量は１〜５wt％であり、図２の鉄−窒素
系状態図を参照すれば、前記拡散層には共析変態が存在
すると共に、その共析温度（Ａ1 変態点）が５９０℃に
なっていることがわかる。なお、前記鉄−窒素化合物層
は主にε相（Ｆe2-3Ｎ）からなっている。良く知られて
いるように、鉄−炭素系のＡ1 変態点は７２３℃であ
り、前記拡散層のＡ1 変態点は、鉄−炭素系のそれより
かなり低く、しかもガス軟窒化処理の常用温度５７０〜
５８０℃に近い温度となっている。Generally, when a gas nitrocarburizing treatment is applied to a steel part, an iron-nitrogen compound layer is formed on the outermost surface, and a nitrogen diffusion layer is formed below the compound layer. in this case,
The nitrogen content of the iron-nitrogen compound layer is 8 to 10 wt% and the nitrogen content of the diffusion layer is 1 to 5 wt%. Referring to the iron-nitrogen phase diagram of FIG. It can be seen that the eutectoid transformation is present and the eutectoid temperature (A 1 transformation point) is 590 ° C. The iron-nitrogen compound layer is mainly composed of an ε phase (Fe 2-3 N). As is well known, the A 1 transformation point of the iron-carbon system is 723 ° C., and the A 1 transformation point of the diffusion layer is considerably lower than that of the iron-carbon system. Temperature 570
The temperature is close to 580 ° C.
【０００９】したがって、本発明のように鋼製部品をガ
ス軟窒化処理後、これを５９０℃以上に加熱すれば、ガ
ス軟窒化処理により形成された窒素の拡散層は部分的に
オーステナイト（γ）組織となり、その温度から急冷す
れば、前記オーステナイトはマルテンサイトに変態する
ようになる。この場合、最表面の鉄−窒素化合物層には
何らの組織的変化も起こらず（図２参照）、しかもその
上限温度は、その鋼のＡ1 変態点未満となっているの
で、心部側でマルテンサイト変態が起こらず、心部側の
靭性が低下することもない。Therefore, if the steel part is heated to 590 ° C. or higher after the gas nitrocarburizing treatment of the steel part as in the present invention, the nitrogen diffusion layer formed by the gas nitrocarburizing treatment is partially austenitic (γ). When it becomes a structure and is rapidly cooled from that temperature, the austenite is transformed into martensite. In this case, iron outermost surface - does not occur even any organizational change in the nitrogen compound layer (see FIG. 2), yet the upper limit temperature is, since a A less than 1 transformation point of the steel, heart side Thus, martensitic transformation does not occur, and the toughness on the core side does not decrease.
【００１０】すなわち、本発明の方法によれば、最表面
の鉄−窒素化合物層および心部側に悪影響を及ぼすこと
なく、窒素の拡散層のみを選択的に硬質層に変化させる
ことができ、これにより打痕に対する抵抗性が可及的に
高められるようになる。That is, according to the method of the present invention, it is possible to selectively change only the nitrogen diffusion layer into a hard layer without adversely affecting the outermost iron-nitrogen compound layer and the core side. Thereby, the resistance to dents can be increased as much as possible.
【００１１】本発明は、ガス軟窒化処理後、一旦常温ま
で冷却した後、５９０℃以上、Ａ1変態点未満の温度範
囲に再加熱しても良いが、熱エネルギーの有効利用を図
るためには、ガス軟窒化処理後、降温させることなくそ
のまま同温度範囲まで加熱するようにするのが望まし
い。In the present invention, after the gas nitrocarburizing treatment, once cooled to room temperature, it may be re-heated to a temperature range of 590 ° C. or more and less than the A 1 transformation point. After the gas nitrocarburizing treatment, it is desirable to heat the gas to the same temperature range without lowering the temperature.
【００１２】本発明で対象する鋼製品は、特にその材種
を問うものではないが、汎用の炭素鋼を対象とした場合
に、打痕に対する抵抗性を顕著に改善することができ
る。[0012] The steel product of the present invention does not particularly matter the grade, but when a general-purpose carbon steel is used, the resistance to dents can be remarkably improved.
【００１３】[0013]
【発明の実施の形態】以下、本発明の実施の形態を添付
図面に基づいて説明する。Embodiments of the present invention will be described below with reference to the accompanying drawings.
【００１４】図１は、本発明に係る鋼製部品の表面硬化
処理における熱サイクルを示したものである。本表面硬
化処理方法の実施に際しては、加熱手段およびガス置換
手段を付設した真空炉を用い、先ず、真空炉内を真空引
きしてその内部に窒素ガス（Ｎ2 ）を導入しながら、標
準の軟窒化処理温度Ｔ1 （５７０〜５８０℃）まで昇温
する。そして、軟窒化処理温度Ｔ1 まで昇温したら、真
空炉内にアンモニア（ＮＨ3 ）と、Ｎ2 と二酸化炭素
（ＣＯ2 ）とを所定の割合（一例として、ＮＨ3：Ｎ
2 ：ＣＯ2 ＝６０：３７：３）で供給し、真空炉内を浸
炭窒化性ガス雰囲気として所定時間Ｈ1 （例えば、２時
間）保持し、いわゆるガス軟窒化処理を行う。このガス
軟窒化処理により、鋼製部品の表面には、鉄−窒素化合
物層と窒素の拡散層とが形成される。FIG. 1 shows a thermal cycle in a surface hardening treatment of a steel part according to the present invention. In carrying out the present surface hardening method, a vacuum furnace equipped with a heating means and a gas replacement means is used. First, the inside of the vacuum furnace is evacuated and nitrogen gas (N 2 ) is introduced into the vacuum furnace. The temperature is raised to the soft nitriding temperature T 1 (570-580 ° C.). Then, when the temperature was raised to soft nitriding treatment temperature T 1, and ammonia (NH 3) in a vacuum furnace, the N 2 and carbon dioxide (CO 2) as a predetermined percentage (example, NH 3: N
2 : CO 2 = 60: 37: 3), and the inside of the vacuum furnace is kept in a carbonitriding gas atmosphere for a predetermined time H 1 (for example, 2 hours) to perform a so-called gas nitrocarburizing treatment. By this gas soft nitriding treatment, an iron-nitrogen compound layer and a nitrogen diffusion layer are formed on the surface of the steel part.
【００１５】上記ガス軟窒化処理を終えたら、炉内の浸
炭窒化性ガスを窒素と置換しながら、炉内温度を５９０
℃以上でかつその鋼に特有のＡ1 変態点（炭素鋼の場合
は７２３℃）未満の温度範囲の適当温度Ｔ2 まで上昇さ
せ、その温度Ｔ2 にわずかな時間Ｈ2 （３〜１０分間程
度）保持した後、真空炉に隣接して設けた油槽内の油中
に鋼製部品を浸漬して急冷し、いわゆる焼入れ処理を行
う。この焼入れ処理により、上記ガス軟窒化処理により
形成された、鉄−窒素化合物層下の窒素の拡散層が部分
的にマルテンサイト組織となり、その硬さが可及的に高
められるようになり、したがって、得られた鋼製部品の
打痕に対する抵抗性は可及的に向上する。なお、本実施
の形態では、炉内の浸炭窒化性ガスを窒素ガスに置換し
た後に焼入れ処理を行っているが、置換せずに焼入れ処
理を行っても差し支えない。After the above gas nitrocarburizing treatment is completed, the temperature in the furnace is set to 590 while replacing the carbonitriding gas in the furnace with nitrogen.
° C. or more and specific A 1 transformation point in the steel is raised to an appropriate temperature T 2 of the temperature range of less than (723 ° C. in the case of carbon steel), the slight time temperature T 2 H 2 (3 to 10 minutes After holding the steel parts, the steel parts are immersed in oil in an oil tank provided adjacent to the vacuum furnace and rapidly cooled to perform a so-called quenching treatment. By this quenching treatment, the nitrogen diffusion layer formed under the iron-nitrogen compound layer formed by the gas nitrocarburizing treatment partially has a martensitic structure, and its hardness is increased as much as possible. The resistance of the obtained steel parts to dents is improved as much as possible. In the present embodiment, the quenching process is performed after the carbonitriding gas in the furnace is replaced with the nitrogen gas, but the quenching process may be performed without replacement.
【００１６】[0016]
実施例１ ＪＩＳ Ｓ２５Ｃ製の油圧緩衝器用ピストンロッド素材
に高周波焼入れおよび焼戻しの調質処理を施した後（表
面硬さＨv ３５０、硬化深さ０．６ｍｍ）、これに必要
な切削加工を加え、さらにその表面をセンタレス研削盤
により研削加工して、所定のロッド寸法（径１０ｍｍ）
に仕上げた。次に、前記ロッドの数百本を一単位として
専用の治具に固定し、バッチ式の洗浄機内にセットして
ロッド表面に付着していた研削油を除去した。その後、
同じ数百本単位のロッドを専用のガス軟窒化炉（真空
炉）に装入し、図１に示した熱サイクルに従ってガス軟
窒化処理および焼入れ処理を行った。この時、ガス軟窒
化処理は、［ＮＨ3 ：Ｎ2 ：ＣＯ2 ＝６０：３７：３］
の浸炭窒化性ガス雰囲気で、温度Ｔ1 ＝５８０℃、時間
Ｈ1 ＝２時間の条件で行い、焼入れ処理は、温度Ｔ2 ＝
６５０℃、時間Ｈ2 ＝５分、油温１１０℃の油中冷却の
条件で行った。そして、この処理後、各ロッドを専用治
具から取り外し、一本ずつバフ研磨を行い、表面粗さＲ
y ＝０．６μｍ以下になるように仕上げ、後述する(A)
顕微鏡観察試験、(B) 硬さ試験、(C) 打痕試験および
(D) 耐食性試験に供した。Example 1 After subjecting a piston rod material for a hydraulic shock absorber made of JIS S25C to a tempering treatment of induction hardening and tempering (surface hardness Hv 350, hardening depth 0.6 mm), necessary cutting work was added thereto. Further, the surface is ground by a centerless grinder to obtain a predetermined rod size (diameter 10 mm).
Finished. Next, several hundreds of the rods were fixed as a unit to a dedicated jig, and set in a batch type washer to remove grinding oil adhering to the rod surface. afterwards,
The same several hundred rods were placed in a dedicated gas nitrocarburizing furnace (vacuum furnace), and gas nitrocarburizing and quenching were performed according to the thermal cycle shown in FIG. At this time, the gas nitrocarburizing treatment is performed by [NH 3 : N 2 : CO 2 = 60: 37: 3].
In the carbonitriding gas atmosphere, the temperature T 1 = 580 ° C., carried out under conditions of time H 1 = 2 hours, quench process, the temperature T 2 =
Cooling in oil was performed at 650 ° C., time H 2 = 5 minutes, and oil temperature was 110 ° C. After this treatment, each rod is removed from the special jig and buffed one by one to obtain a surface roughness R
Finish so that y = 0.6 μm or less.
Microscopic observation test, (B) hardness test, (C) dent test and
(D) It was subjected to a corrosion resistance test.
【００１７】実施例２ Ｓ２５Ｃ製のロッド素材に調質処理を施さずに、いわゆ
る生材のままで用い、これに実施例１と同様のガス軟窒
化処理および焼入れ処理を施し、さらに同様のバフ研磨
を行ってロッドを仕上げ、これを後述の(A) 顕微鏡観察
試験、(B) 硬さ試験、(C) 打痕試験および(D) 耐食性試
験に供した。Example 2 A rod material made of S25C is not subjected to a tempering treatment, but is used as it is as a raw material, and is subjected to the same gas nitrocarburizing treatment and quenching treatment as in the first embodiment, and further to a similar buffing treatment. The rod was polished to finish the rod, which was subjected to (A) a microscopic observation test, (B) a hardness test, (C) a dent test, and (D) a corrosion resistance test described later.
【００１８】比較例１ Ｓ２５Ｃ製のロッド素材に、実施例１と同様の調質処理
を施すと共に、実施例１と同様のガス軟窒化処理を施
し、さらに同様のバフ研磨を行ってロッドを仕上げ、こ
れを後述の(A) 顕微鏡観察試験、(B) 硬さ試験、(C) 打
痕試験および(D)耐食性試験に供した。Comparative Example 1 A rod material made of S25C was subjected to the same refining treatment as in Example 1, the same gas nitrocarburizing treatment as in Example 1, and the same buff polishing to finish the rod. This was subjected to (A) a microscope observation test, (B) a hardness test, (C) a dent test, and (D) a corrosion resistance test described below.
【００１９】比較例２ Ｓ２５Ｃ製のロッド素材に調質処理を施さずに、いわゆ
る生材のままで用い、これに実施例１と同様のガス軟窒
化処理を施し、さらに同様のバフ研磨を行ってロッドを
仕上げ、これを後述の(A) 顕微鏡観察試験、(B) 硬さ試
験、(C) 打痕試験および(D) 耐食性試験に供した。Comparative Example 2 A rod material made of S25C was not subjected to a tempering treatment, but was used as it was, and was subjected to the same gas nitrocarburizing treatment as in the first embodiment, followed by the same buff polishing. The rod was finished with a rod, and the rod was subjected to (A) a microscopic observation test, (B) a hardness test, (C) a dent test, and (D) a corrosion resistance test described later.
【００２０】比較例３ Ｓ２５Ｃ製のロッド素材に、実施例１と同様の調質処理
を施した後、ガス軟窒化処理の温度Ｔ2 として６２０
℃、その時間Ｈ1 として１．５時間を選択する以外は実
施例１と同様のガス軟窒化処理を行い、さらに同様のバ
フ研磨を行ってロッドを仕上げ、これを後述の顕微鏡観
察試験、(B) 硬さ試験および(D) 耐食性試験に供した。Comparative Example 3 After subjecting a rod material made of S25C to the same tempering treatment as in Example 1, the temperature T 2 of the gas nitrocarburizing treatment was set to 620.
° C., subjected to the same gas nitrocarburizing treatment as in Example 1 except that selects for 1.5 hours as its time H 1, finishing rod further by performing the same buffing, microscopic observation test described below it, ( B) Hardness test and (D) Corrosion resistance test.
【００２１】(A) 顕微鏡観察試験 顕微鏡観察試験は、被検鏡面を研磨した腐食液（ナイタ
ール）で腐食する方法によった。その結果、実施例１、
２および比較例３のものには、最表面に１８〜２０μｍ
厚さの鉄−窒素化合物層の存在が認められると共に、そ
の下にマルテンサイト組織の存在が認められたが、比較
例１および２のものには、前記したマルテンサイト組織
の存在は認められなかった。(A) Microscopic Observation Test The microscopic observation test was based on a method of corroding a mirror surface to be inspected with a polished etchant (Nital). As a result, Example 1,
2 and Comparative Example 3, 18 to 20 μm
The presence of a thick iron-nitrogen compound layer was observed, and the presence of a martensite structure was observed below the iron-nitrogen compound layer. However, in Comparative Examples 1 and 2, the presence of the aforementioned martensite structure was not observed. Was.
【００２２】(B) 硬さ試験 硬さ試験は、ビッカース硬度計を用いて、荷重１００gf
の条件で行い、表面から心部側への硬さ分布を求めた。
図３は、その結果を示したもので、これより、本発明に
係る実施例１および２のものは、標準のガス軟窒化処理
を施した比較例１および２のものに比較して、表面側の
０．１ｍｍから心部側の１ｍｍにかけての範囲で硬さが
高くなっていることが明らかである。また、比較例の中
では、高温（６２０℃）で軟窒化処理した比較例３のも
のが、同範囲における硬さが比較的高くなっているが、
これは、鉄−窒素系の状態図（図２）におけるＡ1 変態
点を超えて処理したため、拡散層が部分的にマルテンサ
イト変態したためであると推定される。ただし、この比
較例３のものは、後述の耐食性試験の結果から明らかな
ように耐食性に劣っており、実用上、好ましくないとい
える。なお、参考にあげた調質処理（高周波焼入れ焼戻
し）を施したもの（◆印）は、表面から１ｍｍ程度深さ
まで、ほぼ一定の硬さを有しているが、表面の硬さは各
軟窒化処理を施したものに比べてかなり低く、耐摩耗性
の点で問題が残る。(B) Hardness test The hardness test was carried out using a Vickers hardness tester with a load of 100 gf.
And the hardness distribution from the surface to the core was determined.
FIG. 3 shows the results. The results of Examples 1 and 2 according to the present invention are higher than those of Comparative Examples 1 and 2 subjected to the standard gas nitrocarburizing treatment. It is clear that the hardness is high in the range from 0.1 mm on the side to 1 mm on the core side. Among the comparative examples, the comparative example 3 subjected to the nitrocarburizing treatment at a high temperature (620 ° C.) has a relatively high hardness in the same range.
This iron - for treated beyond the A 1 transformation point in the nitrogen phase diagram (FIG. 2), the diffusion layer is estimated to be due to partially martensitic transformation. However, Comparative Example 3 is inferior in corrosion resistance, as is apparent from the results of the corrosion resistance test described below, and is not preferable in practical use. In addition, the material subjected to the refining treatment (induction quenching and tempering) (marked with ◆) has a substantially constant hardness up to a depth of about 1 mm from the surface. It is considerably lower than the one subjected to the nitriding treatment, and a problem remains in terms of wear resistance.
【００２３】(C) 打痕試験 打痕試験は、ひょう量５kgf-m シャルピー衝撃試験機を
用い、そのハンマー振上角度を種々に変化させて、供試
材としてのロッドを打撃する方法で行い、それぞれにつ
いて打痕深さを測定した。図４は、その結果を示したも
ので、本実施例１および２のものは、比較例１のものに
比べて打痕深さが著しく小さくなっており、参考として
あげた硬質クロムめっきを施したもの（■印）と同等か
それより優れた、打痕に対する抵抗性を示すことが明ら
かとなった。(C) Indentation test The indentation test was performed by using a 5 kgf-m Charpy impact tester with a hammer swing angle varied in various ways and hitting a rod as a test material. The dent depth was measured for each. FIG. 4 shows the results. In Examples 1 and 2, the depth of the dent was significantly smaller than that in Comparative Example 1, and the hard chromium plating as a reference was applied. It was clarified that the composition exhibited resistance to dents equal to or better than that obtained by the test (marked by ■).
【００２４】(D) 耐食性試験 耐食性試験は、ＪＩＳ Ｚ２３７１塩水噴霧試験に基づ
いて行い、供試材としてのロッドそれぞれについて、腐
食面積率からテーティングナンバー（ＪＩＳＨ８５０
２）を求めた。図５は、その結果を示したもので、本実
施例１および２のものは、その評価点（SST96h,RN ）が
標準のガス軟窒化処理を施した比較例１および２のもの
と同じであり、耐食性の点で問題がないことが明らかと
なった。なお、比較例の中では、高温で軟窒化処理を施
した比較例３のものが、他の比較例のものに比べて耐食
性に劣っている。(D) Corrosion resistance test The corrosion resistance test was carried out based on the JIS Z2371 salt spray test.
2) was determined. FIG. 5 shows the results. The evaluation points (SST96h, RN) of Examples 1 and 2 are the same as those of Comparative Examples 1 and 2 in which standard gas nitrocarburizing treatment was performed. There was no problem in terms of corrosion resistance. In addition, among the comparative examples, those of the comparative example 3 subjected to the nitrocarburizing treatment at a high temperature are inferior in corrosion resistance to those of the other comparative examples.
【００２５】[0025]
【発明の効果】上記したように、本発明に係る鋼製部品
の表面硬化処理方法によれば、ガス軟窒化処理の特長で
ある耐摩耗性および耐食性の良さを犠牲にすることな
く、打痕に対する抵抗性を可及的に高めることができ、
その利用価値は大なるものがある。As described above, according to the surface hardening method for steel parts according to the present invention, the dents are formed without sacrificing the good wear resistance and corrosion resistance characteristic of the gas nitrocarburizing treatment. Resistance as much as possible,
Its utility value is great.
【図１】本発明に係る表面硬化処理における熱サイクル
を示すグラフである。FIG. 1 is a graph showing a heat cycle in a surface hardening treatment according to the present invention.
【図２】鉄−窒素系の相関係を示す状態図である。FIG. 2 is a phase diagram showing a phase relationship between iron and nitrogen.
【図３】本発明の実施例の表面硬さ分布を比較例と対比
して示すグラフである。FIG. 3 is a graph showing a surface hardness distribution of an example of the present invention in comparison with a comparative example.
【図４】本発明の実施例の打痕試験結果を比較例と対比
して示すグラフである。FIG. 4 is a graph showing the results of a dent test of an example of the present invention in comparison with a comparative example.
【図５】本発明の実施例の耐食性試験結果を比較例と対
比して示す図表である。FIG. 5 is a table showing the results of a corrosion resistance test of examples of the present invention in comparison with comparative examples.
Claims (2)
窒化処理した後、該鋼製部品を５９０℃以上でかつその
鋼に特有のＡ1 変態点未満の温度範囲に加熱し、続いて
急冷することを特徴とする鋼製部品の表面硬化処理方
法。1. After gas-nitriding a steel part at a temperature lower than 590 ° C., the steel part is heated to a temperature range of 590 ° C. or higher and lower than the A 1 transformation point specific to the steel, Surface quenching method for steel parts characterized by rapid cooling.
鋼製部品を５９０℃以上、Ａ1 変態点未満の温度範囲に
加熱することを特徴とする請求項１に記載の表面硬化処
理方法。2. The surface hardening method according to claim 1, wherein after the gas nitrocarburizing treatment, the steel part is heated to a temperature range of 590 ° C. or higher and lower than the A 1 transformation point without lowering the temperature.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP21984397A JPH1150141A (en) | 1997-07-31 | 1997-07-31 | Surface hardening treatment for steel parts |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP21984397A JPH1150141A (en) | 1997-07-31 | 1997-07-31 | Surface hardening treatment for steel parts |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH1150141A true JPH1150141A (en) | 1999-02-23 |
Family
ID=16741939
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP21984397A Pending JPH1150141A (en) | 1997-07-31 | 1997-07-31 | Surface hardening treatment for steel parts |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH1150141A (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002302756A (en) * | 2001-01-31 | 2002-10-18 | Tokico Ltd | Surface treated steel member and gas soft nitriding method |
| KR100988702B1 (en) * | 2006-12-14 | 2010-10-18 | 유겐가이샤 유키코슈하 | A quenched nitride and the method of manufacture thereof |
| JP2014111821A (en) * | 2012-11-02 | 2014-06-19 | Oita Univ | Hardening treatment method of low alloy steel |
| JP2014122367A (en) * | 2012-12-20 | 2014-07-03 | Daido Steel Co Ltd | Vacuum nitriding treatment method |
| CN103925306A (en) * | 2013-01-15 | 2014-07-16 | 株式会社捷太格特 | Sliding Member, Clutch Plate, And Production Methods Thereof |
-
1997
- 1997-07-31 JP JP21984397A patent/JPH1150141A/en active Pending
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002302756A (en) * | 2001-01-31 | 2002-10-18 | Tokico Ltd | Surface treated steel member and gas soft nitriding method |
| KR100988702B1 (en) * | 2006-12-14 | 2010-10-18 | 유겐가이샤 유키코슈하 | A quenched nitride and the method of manufacture thereof |
| JP2014111821A (en) * | 2012-11-02 | 2014-06-19 | Oita Univ | Hardening treatment method of low alloy steel |
| JP2014122367A (en) * | 2012-12-20 | 2014-07-03 | Daido Steel Co Ltd | Vacuum nitriding treatment method |
| CN103925306A (en) * | 2013-01-15 | 2014-07-16 | 株式会社捷太格特 | Sliding Member, Clutch Plate, And Production Methods Thereof |
| US20140197003A1 (en) * | 2013-01-15 | 2014-07-17 | Cnk Co., Ltd. | Sliding member, clutch plate, and production methods thereof |
| JP2014136811A (en) * | 2013-01-15 | 2014-07-28 | Jtekt Corp | Sliding member, clutch plate and production methods thereof |
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