JPH02159478A - Piston ring - Google Patents
Piston ringInfo
- Publication number
- JPH02159478A JPH02159478A JP31434788A JP31434788A JPH02159478A JP H02159478 A JPH02159478 A JP H02159478A JP 31434788 A JP31434788 A JP 31434788A JP 31434788 A JP31434788 A JP 31434788A JP H02159478 A JPH02159478 A JP H02159478A
- Authority
- JP
- Japan
- Prior art keywords
- layer
- titanium nitride
- piston ring
- nitride film
- hardness
- 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.)
- Granted
Links
- 239000010410 layer Substances 0.000 claims abstract description 89
- NRTOMJZYCJJWKI-UHFFFAOYSA-N Titanium nitride Chemical compound [Ti]#N NRTOMJZYCJJWKI-UHFFFAOYSA-N 0.000 claims abstract description 64
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims abstract description 46
- 239000002344 surface layer Substances 0.000 claims abstract description 35
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 23
- 238000007733 ion plating Methods 0.000 claims abstract description 16
- 150000004767 nitrides Chemical class 0.000 claims abstract description 10
- 230000002093 peripheral effect Effects 0.000 claims description 21
- 238000010301 surface-oxidation reaction Methods 0.000 claims description 2
- 238000000034 method Methods 0.000 abstract description 4
- 238000005299 abrasion Methods 0.000 abstract 4
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N Titan oxide Chemical compound O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 abstract 2
- OGIDPMRJRNCKJF-UHFFFAOYSA-N titanium oxide Inorganic materials [Ti]=O OGIDPMRJRNCKJF-UHFFFAOYSA-N 0.000 abstract 2
- 238000012360 testing method Methods 0.000 description 63
- 239000010408 film Substances 0.000 description 57
- 239000000463 material Substances 0.000 description 20
- 239000007789 gas Substances 0.000 description 15
- 229910001220 stainless steel Inorganic materials 0.000 description 15
- 239000010935 stainless steel Substances 0.000 description 15
- 238000005121 nitriding Methods 0.000 description 12
- 229910000734 martensite Inorganic materials 0.000 description 11
- 230000013011 mating Effects 0.000 description 11
- 230000003746 surface roughness Effects 0.000 description 10
- 239000011248 coating agent Substances 0.000 description 9
- 238000000576 coating method Methods 0.000 description 9
- 238000010586 diagram Methods 0.000 description 9
- 238000007747 plating Methods 0.000 description 8
- 238000012545 processing Methods 0.000 description 8
- 238000005498 polishing Methods 0.000 description 7
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 5
- 229910001651 emery Inorganic materials 0.000 description 5
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 4
- 239000010687 lubricating oil Substances 0.000 description 4
- 239000003921 oil Substances 0.000 description 4
- 238000004381 surface treatment Methods 0.000 description 4
- 239000010936 titanium Substances 0.000 description 4
- 229910052719 titanium Inorganic materials 0.000 description 4
- 238000005422 blasting Methods 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 229910001018 Cast iron Inorganic materials 0.000 description 2
- 230000000573 anti-seizure effect Effects 0.000 description 2
- 239000000919 ceramic Substances 0.000 description 2
- 239000002131 composite material Substances 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000006073 displacement reaction Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000000446 fuel Substances 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 239000000843 powder Substances 0.000 description 2
- 229910017060 Fe Cr Inorganic materials 0.000 description 1
- 229910002544 Fe-Cr Inorganic materials 0.000 description 1
- UPHIPHFJVNKLMR-UHFFFAOYSA-N chromium iron Chemical compound [Cr].[Fe] UPHIPHFJVNKLMR-UHFFFAOYSA-N 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000001704 evaporation Methods 0.000 description 1
- 230000008020 evaporation Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 239000010705 motor oil Substances 0.000 description 1
- -1 rotating at 5200rpm Substances 0.000 description 1
- 239000004575 stone Substances 0.000 description 1
- 239000010409 thin film Substances 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Landscapes
- Pistons, Piston Rings, And Cylinders (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は耐摩耗性、耐焼付性に優れ、且つ初期馴染み性
に優れた皮膜を形成した内燃機関用ピストンリングに関
する。DETAILED DESCRIPTION OF THE INVENTION [Field of Industrial Application] The present invention relates to a piston ring for an internal combustion engine on which a film is formed that has excellent wear resistance, seizure resistance, and initial conformability.
従来、ピストンリングの外周摺動面の表面処理としでは
、硬質クロムめっきが主に使用されている。硬質クロム
めっきを被覆したピストンリングは、自身の耐摩耗性に
優れ、相手シリンダの摩耗も少ないことから、長い間ピ
ストンリングの表面処理の主流をなしてきた。Conventionally, hard chrome plating has been mainly used as a surface treatment for the outer peripheral sliding surface of piston rings. Piston rings coated with hard chrome plating have long been the mainstream surface treatment for piston rings because they have excellent wear resistance and cause less wear on the mating cylinder.
しかしながら、近年エンジンの高出力化、高回転化に伴
い、ピストンリングが晒される環境は益々苛酷になって
おり、このような環境下では従来の硬質クロムめっきで
は対処できなくなりつつあり、−層強力な耐摩耗性能及
び耐焼付性能を持つピストンリングが要求されるように
なってきた。However, as engines have become more powerful and rotated in recent years, the environment to which piston rings are exposed has become increasingly harsh, and conventional hard chrome plating is no longer able to cope with this environment. There is a growing demand for piston rings with excellent wear resistance and seizure resistance.
かかる状況に対処するため、Ｆａ−Ｃｒ系プラズマ溶射
ピストンリング、ステンレス製窒化処理ピストンリング
、セラミック系粉末複合めっきピストンリング等が開発
され、一部のエンジンで採用されている。In order to cope with this situation, Fa-Cr based plasma sprayed piston rings, stainless steel nitrided piston rings, ceramic powder composite plated piston rings, etc. have been developed and are used in some engines.
〔発明が解決しようとする課題〕
これらの技術によれば、耐摩耗性及び耐焼付性の点で、
従来技術による硬質クロム、めっきに比し、はるかに改
善されたが、次のような不具合が見出されている。[Problems to be solved by the invention] According to these techniques, in terms of wear resistance and seizure resistance,
Although this method is much improved compared to conventional hard chrome plating, the following problems have been discovered.
Ｆｅ−Ｃｒ系プラズマ溶射ピストンリングは、優れた耐
摩耗性及び耐焼付性を持つが、反面相手シリンダ材の摩
耗が多いという欠点があり、また腐食雰囲気下に晒され
ると、溶射層が母材より剥離しやすいという弱点をもつ
。Fe-Cr based plasma sprayed piston rings have excellent wear resistance and seizure resistance, but on the other hand, they have the disadvantage of causing a lot of wear on the mating cylinder material, and when exposed to a corrosive atmosphere, the sprayed layer deteriorates to the base material. It has the disadvantage of being more easily peeled off.
セラミック系粉末複合めっきピストンリングは、優れた
耐焼付性を持つものの、マトリックスの強度に問題があ
り、エンジン運転中においてめっきの割れ、剥離が発生
しやすいという欠点をもつ。Although ceramic powder composite plating piston rings have excellent seizure resistance, they have problems with the strength of the matrix, and the plating tends to crack and peel during engine operation.
ステンレス製窒化処理ピストンリングは、優れた耐摩耗
性能を持ち、且つ相手材の摩耗も少ないという優れた摩
耗特性を持つものの、耐焼付性が低く、熱負荷の高いエ
ンジンでは問題の出ることがある。Stainless steel nitrided piston rings have excellent wear resistance and less wear on the mating material, but they have low seizure resistance and can cause problems in engines with high heat loads. .
ステンレス製窒化処理ピストンリングでは、かかる状況
に対処するため、外周摺動面に更にイオンプレーティン
グにより所定厚さを有する窒化チタン皮膜を被覆する技
術が開示されている。しかし、現在使用されている窒化
チタン皮膜は相手材へのなじみ性が悪く、且つ表面粗さ
が０．６μｍＲ２より大きくなると、相手材攻撃性が急
激に高くなることが判明している。In order to deal with this situation, a technique has been disclosed for stainless steel nitrided piston rings in which the outer peripheral sliding surface is further coated with a titanium nitride film having a predetermined thickness by ion plating. However, it has been found that the currently used titanium nitride film has poor compatibility with the mating material, and when the surface roughness is greater than 0.6 μmR2, the aggressiveness of the titanium nitride film to the mating material increases rapidly.
本発明は以上の点に鑑みてなされたものであり、窒化チ
タン皮膜の初期摩耗をコントロールし、初期馴染み性を
良くして、早期にシリンダボアを馴染ませた後、耐摩耗
性、耐焼付性に優れた窒化チタン皮膜層を摺動させるよ
うにしたピストンリングを提供することを目的とする。The present invention has been made in view of the above points, and it is possible to control the initial wear of the titanium nitride film, improve the initial fit, and improve the wear resistance and seizure resistance after fitting the titanium nitride film into the cylinder bore at an early stage. An object of the present invention is to provide a piston ring on which an excellent titanium nitride film layer slides.
本発明のピストンリングは、少なくとも外周摺動面に窒
化チタン（Ｔ１）ＩＮＹ）皮膜を形成したピストンリン
グにおいて、少なくとも外周摺動面の窒化チタン皮膜層
の靭性を表層に向かうに従い徐々に低くし、表層部は窒
素濃度を高（して脆くしたことを特徴とする。The piston ring of the present invention is a piston ring in which a titanium nitride (T1) INY) film is formed on at least the outer peripheral sliding surface, and the toughness of the titanium nitride film layer on at least the outer peripheral sliding surface is gradually lowered toward the surface layer, The surface layer is characterized by a high nitrogen concentration, making it brittle.
あるいは、少なくとも外周摺動面に窒化チタン（Ｔ ｌ
＊Ｎｖ ）皮膜を形成したピストンリングにおいて、
少なくとも外周摺動面の窒化チタン皮膜層の窒素濃度を
表層に向かうに従い徐々に低くし、表層部の硬さをＨｖ
ｌ ８００以下にしたことを特徴とする。Alternatively, at least the outer peripheral sliding surface is made of titanium nitride (T l
*Nv) In a piston ring with a film formed,
The nitrogen concentration of the titanium nitride film layer on at least the outer peripheral sliding surface is gradually lowered toward the surface layer, and the hardness of the surface layer is reduced to Hv.
l 800 or less.
そして、窒化チタン皮膜の内側に窒化層を形成するのが
好ましい、そしてこの窒化層は表面酸化層及び白層を除
去した層であるのが好ましい。It is preferable to form a nitride layer inside the titanium nitride film, and this nitride layer is preferably a layer from which the surface oxidation layer and white layer have been removed.
そして、窒化チタン皮膜の被覆はイオンプレーティング
によるのが好ましい。The titanium nitride film is preferably coated by ion plating.
ピストンリング表面に、本発明の窒化チタン皮膜を被覆
する場合は５００℃以下、好ましくは３５０℃以下で処
理するのが好ましい、第３図に、窒化処理層の加熱（各
温度に１時間保持）による硬さの変化を示す特性曲線図
を示す０図中、窒化処理層はマルテンサイト系１７Ｃｒ
ステンレス製ピストンリング母材に窒化処理を施し、表
面の酸化層及び白層を除去したものである。第３図より
、窒化処理層は、５００℃以下の加熱では硬さの低下は
ほとんどみられない。When the piston ring surface is coated with the titanium nitride film of the present invention, it is preferable to perform the treatment at a temperature of 500°C or lower, preferably 350°C or lower. Figure 3 shows the heating of the nitrided layer (maintained at each temperature for 1 hour). In Figure 0, which shows a characteristic curve diagram showing changes in hardness due to
The stainless steel piston ring base material is nitrided to remove the oxide layer and white layer on the surface. From FIG. 3, the nitrided layer shows almost no decrease in hardness when heated at 500° C. or lower.
一般に、窒化チタン皮膜は耐摩耗性、耐焼付性に優れる
ことが知られているが、高硬度故に自身の表面粗さが大
きくなるに従い、相手材摩耗が急増する欠点がある。そ
れゆえに、窒化チタン皮膜表面の粗さを０．６μｍＲｚ
以下にしたり、ピストンリング外周表面形状を滑らかな
、大きなＲ形状にして局部的に高面圧が発生しないよう
な処置が必要となる。しかしながら、これらの処置を施
しても、高温、高圧下においては、耐焼付性は優れるも
のの、相手材摩耗が多いという欠点を有する。Generally, titanium nitride films are known to have excellent wear resistance and seizure resistance, but due to their high hardness, they have the disadvantage that as their surface roughness increases, wear on the mating material increases rapidly. Therefore, the roughness of the titanium nitride film surface is set to 0.6μmRz
It is necessary to take measures to prevent local high surface pressure from occurring by making the piston ring's outer circumferential surface shape smooth and with a large radius. However, even if these measures are taken, although the seizure resistance is excellent under high temperature and high pressure conditions, there is a drawback that there is a lot of wear on the mating material.
また、ピストンリング、ピストンが充分に馴染まないう
ちに、シリンダ内周面が鏡面化した場合、窒化チタン皮
膜を持たない他のピストンリングやピストン、シリンダ
にスカッフィングが発生する場合がある。Furthermore, if the inner circumferential surface of the cylinder becomes mirror-finished before the piston rings and pistons are fully adapted, scuffing may occur on other piston rings, pistons, and cylinders that do not have a titanium nitride film.
これに比べ、本発明のピストンリングは、窒化チタン皮
膜の表層が脆いか、あるいは硬さを低くしているので、
エンジン運転初期において、早期に窒化チタン皮膜の表
層部が摩耗し、良好な摺動面形状が形成され、その後耐
摩耗性に優れた窒化チタン皮膜層が摺動するために、シ
リンダ内周面の初期摩耗が少なく、且つ耐焼付性、耐摩
耗性に優れる。In contrast, in the piston ring of the present invention, the surface layer of the titanium nitride film is brittle or has low hardness.
In the early stages of engine operation, the surface layer of the titanium nitride film wears out at an early stage, forming a good sliding surface shape, and then the titanium nitride film layer, which has excellent wear resistance, slides on the inner surface of the cylinder. Low initial wear and excellent seizure resistance and wear resistance.
そして、耐焼付性能は従来の窒化チタン皮膜よりも優れ
ていることが基礎・実機性能評価で確認された。これは
初期摩耗が速いために、初期の局部光たり（ミクロ的視
野での金属接触）を回避するために耐焼付性能が向上し
たものと考えられる。Basic and actual machine performance evaluations confirmed that the anti-seizure performance was superior to that of conventional titanium nitride films. This is thought to be due to the fact that the initial wear is rapid, and the anti-seizure performance is improved in order to avoid the initial local flashing (metal contact in a microscopic field).
窒化チタン皮膜の被覆をイオンプレーティングで行うの
は、ピストンリング母材の軟化を防ぎ、母材の耐摩耗性
能を損なうことがないような温度で処理する必要がある
こと、また変形を防止する上からも処理温度は低い方が
望ましいためである。The reason why the titanium nitride film is coated by ion plating is that it must be treated at a temperature that prevents the piston ring base material from softening and does not impair the wear resistance of the base material, and also prevents deformation. This is because it is desirable that the processing temperature be lower.
また、窒化チタン皮膜の窒素濃度（硬さ）を自由にコン
トロールできることによる。Another advantage is that the nitrogen concentration (hardness) of the titanium nitride film can be controlled freely.
第１図と第２図はそれぞれ本発明のピストンリングの断
面図を示す。1 and 2 each show a cross-sectional view of a piston ring of the present invention.
第１図はマルテンサイト系１７Ｃｒステンレス材のピス
トンリング１０１の外周摺動面に窒化チタン皮膜１０２
を被覆形成したもので、第２図はマルテンサイト系１７
Ｃｒステンレス材のとストンリング１０１の全表面にガ
ス窒化層を形成し、その窒化層の表面酸化層及び白層を
除去した層１０３の外周摺動面上に窒化チタン皮膜１０
２を被覆形成したものである。そして窒化チタン皮膜１
０２は、窒化チタン皮膜層の靭性を表層に向かうに従い
徐々に低くし、表層部は窒素濃度を高くして脆くするか
、窒化チタン皮膜層の窒素濃度を表層に向かうに従い徐
々に低くし、表層部の硬さをＨｖｌ ８００以下にして
いる。Figure 1 shows a titanium nitride coating 102 on the outer peripheral sliding surface of a piston ring 101 made of martensitic 17Cr stainless steel.
Figure 2 shows martensitic 17
A gas nitrided layer is formed on the entire surface of the stone ring 101 made of Cr stainless steel material, and a titanium nitride film 10 is formed on the outer peripheral sliding surface of the layer 103 from which the surface oxidized layer and white layer of the nitrided layer are removed.
2 is coated. And titanium nitride film 1
02, the toughness of the titanium nitride film layer is gradually lowered toward the surface layer, and the nitrogen concentration is increased in the surface layer to make it brittle, or the nitrogen concentration of the titanium nitride film layer is gradually lowered toward the surface layer, and the surface layer is made brittle. The hardness of the parts is set to Hvl 800 or less.
（試験１）
第４図は、試験に使用した往復動摩擦試験機の概要を示
す。(Test 1) Figure 4 shows an outline of the reciprocating friction testing machine used in the test.
第４図において、ピストンリングに相当する上試験片ｌ
は、上試験片固定ブロック２により保持され、上方から
油圧シリンダ３により下向きの荷重が加えられる。一方
、シリンダに相当する相手部材たる下試験片４は可動ブ
ロック５により保持され、図示の如きクランク機構６に
より矢印方向に往復動せしめられる。また、７はロード
セルである。第４図に示す摩擦試験機は公知であり、ま
たその構成自体は本発明とは直接関係ないので、詳しい
説明は省略する。In Figure 4, the upper test piece l corresponding to the piston ring
is held by the upper test piece fixing block 2, and a downward load is applied from above by a hydraulic cylinder 3. On the other hand, a lower test piece 4, which is a mating member corresponding to a cylinder, is held by a movable block 5 and is reciprocated in the direction of the arrow by a crank mechanism 6 as shown. Further, 7 is a load cell. The friction tester shown in FIG. 4 is well known, and its configuration itself is not directly related to the present invention, so a detailed explanation will be omitted.
上試験片１の摩耗量は第５図（Ａ）に示す如く、上試験
片１の試験前形状８と試験後形成９を測定し、その差を
測定することにより算出する。下試験片４の摩耗量は第
５図（Ｂ）に示す如く、離間する３ヶ所ａ、ｂ、ｃの凹
み量を測定し、その平均値で示す。The wear amount of the upper test piece 1 is calculated by measuring the pre-test shape 8 and post-test shape 9 of the upper test piece 1 and measuring the difference, as shown in FIG. 5(A). The amount of wear on the lower test piece 4 was determined by measuring the amounts of dents at three separate locations a, b, and c, as shown in FIG. 5(B), and is expressed as the average value.
試験条件は以下の通りである。The test conditions are as follows.
１、供試試料
Ａ、下試験片４ニジリンダブロック用鋳鉄製（ＦＣ２５
相当材）平板（寸法：長さ７０ｍｍ１幅１７ｍｍ、厚さ
１４ｍｍ）の試験面をパフ研磨し、面粗さを０．１μｍ
以下にしたもの、なお、硬さはＨＩＢ９０である。1. Test sample A, lower test piece 4 Cast iron for cylinder block (FC25
Puff polish the test surface of a flat plate (dimensions: length 70 mm, width 17 mm, thickness 14 mm) to obtain a surface roughness of 0.1 μm.
The hardness is HIB90.
Ｂ、上試験片ｌ：マルテンサイト系１７Ｃｒステンレス
材のピストンリング用棒（寸法：直径８ ｍ ｍ ｓ長
さ２３ｍｍ）を母材として以下の表面処理を施した試料
を調整した。B. Upper test piece 1: A sample was prepared using a piston ring rod made of martensitic 17Cr stainless steel (dimensions: diameter 8 mm, length 23 mm) as a base material and subjected to the following surface treatment.
試料！、 （従来技術）−上試験片Ｉ端面を１８ｍｍ
Ｒの球面加工後ガス窒化処理し、
再度１８ｍｍＲの球面加工により表面
の酸化層及び白層を取り除き、パフ研
磨仕上げしたものである。なお、窒化
層の厚さは９０μｍで、硬さはＨｖ１
２００である。sample! , (Prior art) - Upper test piece I end face 18 mm
After processing the R spherical surface, gas nitriding was performed, and the oxide layer and white layer on the surface were removed by 18 mm R spherical processing again, and the product was finished with puff polishing. Note that the thickness of the nitrided layer is 90 μm, and the hardness is Hv1 200.
試料２． （従来技術）−上試験片１端面を１８ｍ ｍ
Ｒの球面加工後ガス窒化処理し、再度１８ｍｍＨの球
面加工により表面
の酸化層及び白層を取り除き、パフ研
ＦＩＩ後イオンプレーティングにより、窒化チタン皮膜
を被覆したもの、窒化層
の厚さは９０μｍ、硬さはＨｖＬ２０
０で、窒化チタン皮膜の硬さはＨｖ２
４００、厚さは２．５μｍである。Sample 2. (Prior art) - Upper test piece 1 end face 18 mm
After processing the R spherical surface, gas nitriding was performed, the oxidized layer and white layer on the surface were removed by spherical processing at 18 mmH, and a titanium nitride film was coated by ion plating after puff polishing FII. The thickness of the nitrided layer was 90 μm. , the hardness is HvL200, and the hardness of the titanium nitride film is Hv2400, and the thickness is 2.5 μm.
試料３． （本発明）−上試験片１端面を１８ｍｍＲの
球面加工後ガス窒化処理し、再
度１９ｍｍＨの球面加工により表面の
酸化層及び白層を取り除き、パフ研磨
後イオンプレーティングにより、窒化
チタン皮膜を被覆したもの、ただし、
被覆時の炉内圧（窒素分圧）を随時変
化させて、窒化チタン皮膜層の靭性を
表層に向かうに従い徐々に低くし、表
層部は窒素濃度を高くし、脆くしたも
のである。窒化層の厚さは９０μｍ、
硬さはＨｖｌ２００で、窒化チタン皮
膜の表面硬さはＨｖ２０００、厚さは
２．５μｍである。Sample 3. (Present invention) - The end face of the upper test piece was processed into a 18 mm radius spherical surface, then subjected to gas nitriding treatment, and the oxide layer and white layer on the surface were removed by 19 mm radius spherical processing again, and after puff polishing, a titanium nitride film was coated by ion plating. However, by changing the furnace pressure (nitrogen partial pressure) during coating, the toughness of the titanium nitride film layer is gradually lowered toward the surface layer, and the nitrogen concentration is increased in the surface layer, making it brittle. be. The thickness of the nitride layer is 90 μm and the hardness is Hvl 200, and the surface hardness of the titanium nitride film is Hv 2000 and the thickness is 2.5 μm.
試料４． （本発明）−上試験片１端面を１８ｍｍＲの
球面加工後ガス窒化処理し、再
度１８ｍｍＨの球面加工により表面の
酸化層及び白層を取り除き、パフ研磨
後イオンプレーティングにより、窒化
チタン皮膜を被覆したもの、ただし、
被覆時の炉内圧（窒素分圧）を随時変
化させて、窒化チタン皮膜層の窒素濃
度を表層に向かうに従い徐々に低くし
、表層部の硬さをＨｖｌ ８００以下にしたものである
。窒化層の厚さは９０
μｍ１硬さはＨｖｌ ２００で、窒化チタン皮膜の表面
硬さはＨｖｌ ７８０、厚さは２．５μｍである。Sample 4. (Present invention) - The end face of the upper test piece was processed into a 18 mm radius spherical surface, then subjected to gas nitriding treatment, and the oxidized layer and white layer on the surface were removed by 18 mm radius spherical processing again, and after puff polishing, a titanium nitride film was coated by ion plating. However, by changing the furnace pressure (nitrogen partial pressure) during coating, the nitrogen concentration of the titanium nitride film layer is gradually lowered toward the surface layer, and the hardness of the surface layer is reduced to Hvl 800 or less. It is. The thickness of the nitrided layer is 90 μm, the hardness is Hvl 200, and the surface hardness of the titanium nitride film is Hvl 780, and the thickness is 2.5 μm.
２、窒化チタン−イオンプレーティング皮膜の製造方法
。2. Method for producing titanium nitride-ion plating film.
使用装置：イオンプレーティング装置
処理条件；■真空中き−Ｉ Ｘ ｌ Ｏ””Ｔｏｒｒ■
ヒータ加熱
■イオンボンバービー−Ａｒガス
中で１５分
■真空中き−Ｉ Ｘ １０−’Ｔｏｒｒ■Ｔｉ溶解
＊■Ｎ２ガス導入−−蒸着−−炉内
圧Ｉ Ｘ ｌ Ｏ−３〜５ Ｘ １０−’Ｔｒｒ
■冷却
■真空槽を大気状態にする。−一
ワーク取り出し。Equipment used: Ion plating equipment Processing conditions: ■Vacuum - IXlO""Torr■
Heater heating - Ion bomber - 15 minutes in Ar gas - Vacuum - I 'Trr ■Cooling■ Bring the vacuum chamber to atmospheric condition. -Take out a workpiece.
＊試料２（従来技術）−炉内圧（Ｎよ、ガス分圧）３〜
５ Ｘ Ｉ Ｏ−’Ｔｏｒｒ
本試料３（本発明ンー炉内圧（Ｎ ｔガス分圧）３〜５
Ｘ １０−’Ｔｏｒｒ −−４Ｑ分Ｉ Ｘ １０−４
Ｔｏｒｒ −−３０分５ Ｘ １０−”Ｔｏｒｒ −−
２０分３Ｘ１０−”Ｔｏｒｒ −１５分
Ｉ Ｘ １０−’Ｔｏｒｒ −−１０分本試料４（本発
明）−炉内圧（ＮＺガス分圧）３ Ｘ ｌ Ｏ−’Ｔｏ
ｒｒ −４０分５ Ｘ １０−’Ｔｏｒｒ −−３Ｑ
分７ Ｘ １０−’Ｔｏｒｒ −−３０分ｌ Ｘ １０
−’Ｔｏｒｒ −−１５分なお、上記試料３．４の各条
件（炉内圧）においてはＴＩの蒸発レートは一定とした
。*Sample 2 (prior art) - Furnace pressure (N, gas partial pressure) 3~
5
X 10-'Torr --4Q min I X 10-4
Torr --30 minutes 5 x 10-"Torr --
20 minutes 3X10-''Torr -15 minutes I
rr -40 minutes 5 X 10-'Torr --3Q
7 minutes x 10-'Torr --30 minutes l x 10
-'Torr--15 minutes The evaporation rate of TI was kept constant under each condition (inner furnace pressure) of Sample 3.4.
３、摩耗試験条件
試験装置：往復動摩擦試験機（第４図参照）試験条件：
ならし２にｇｆ Ｘ １００ｃｐｍ ｘ ５ｗｉ本試験
１０Ｋｇｔ ｘ５００ｃｐ＋ｓ Ｘ １Ｈｒ
（いずれもストロークは５０ｍｍ）
潤滑油ＪＩＳ２号軽油（ミスト状
吹き付け３ｃｃ／ｍ１ｎ）
試験結果：第６図に示すように、窒化チタン皮膜を被覆
した試料２．３．４は
窒化層のみの試料１に比べていず
れも良好な耐摩耗性能を示した。3. Wear test conditions Test equipment: Reciprocating friction tester (see Figure 4) Test conditions:
For break-in 2, gf The coated samples 2.3.4 all showed better wear resistance performance than sample 1 with only a nitrided layer.
そして、試料３，４ （本発明）は 初期には試料２（従来技術）に比 べやや摩耗が多いものの、時間の 経過と共に同等の摩耗量となった 、また相手材の摩耗量は窒化チタ ン皮膜を被覆した試料２（従来技 術）が最も多く、窒化チタン皮膜 を被覆した試料３，４（本発明） は窒化層のみの試料ｌと同等の摩 耗値を示し、相手材摩耗は良好な 性能を示した。And samples 3 and 4 (invention) are Initially, compared to sample 2 (conventional technology) Although there is a lot of wear and tear, over time The amount of wear became the same over time. , and the wear amount of the mating material is titanium nitride. Sample 2 coated with a thin film (conventional technique) titanium nitride film Samples 3 and 4 (invention) coated with is the same friction as sample 1 with only nitride layer. It shows the wear value, and the wear of the mating material is good. demonstrated performance.
（試験２）
第７〜８図は、耐焼付試験に使用したビン・ディスク型
高面圧摩擦試験機の概要を示す。(Test 2) Figures 7 and 8 show an outline of the bottle-disk type high surface pressure friction testing machine used in the seizure resistance test.
ステータ２０に取り外し可能に取り付けられた直径８０
ｍｍの円板２１ （摺動相手部材）の中央には、裏側か
ら注油孔２２を通して潤滑油が注油される。また、ステ
ータ２０は油圧装置により所定圧力でロータ２３側に押
し付けられ、圧力Ｐが作用するようになっている。ステ
ータ２０に相対向してロータ２３が配され、該ロータ２
３は駆動装置によって所定速度で回転する。diameter 80 removably attached to stator 20
Lubricating oil is applied to the center of the mm disc 21 (sliding partner member) from the back side through the oil filling hole 22. Further, the stator 20 is pressed against the rotor 23 at a predetermined pressure by a hydraulic system, so that a pressure P is applied thereto. A rotor 23 is disposed opposite to the stator 20, and the rotor 23 is arranged opposite to the stator 20.
3 rotates at a predetermined speed by a drive device.
ロータ２３の円１２１に対向する端面には試料保持具２
４が設けられていて、該試料保持具２４には同心円上に
等間隔をなして正方形の摺動面を有する４個の試験片２
５が取り付けられ、該摺動面が円板（ステータ）に対接
摺動する。A sample holder 2 is provided on the end surface of the rotor 23 facing the circle 121.
4, and the sample holder 24 has four test pieces 2 having square sliding surfaces arranged at equal intervals on a concentric circle.
5 is attached, and the sliding surface slides against the disc (stator).
このような装置において、摺動面に所定量の給油をしな
がら、ロータ２３を回転させる。一定時間毎にステータ
２０に作用する圧力を段階的に増加させ、円板２１と試
験片２５との摺動により発生する摩擦力をトルクＴとし
てワイヤーを介してロードセル２６に作用させ、その変
化を動歪計２７で読み、記録計２８に記録させる。焼き
付き現象が発生するとトルクＴが急激に上昇する。した
がって、トルクＴが急激に上昇するときに摺動接触面に
作用、している接触面圧を焼き付き発生面圧とし、この
焼き付き発生面圧の大小で焼き付き特性の良否を判定す
る。In such a device, the rotor 23 is rotated while a predetermined amount of oil is supplied to the sliding surface. The pressure applied to the stator 20 is increased stepwise at regular intervals, and the frictional force generated by the sliding between the disk 21 and the test piece 25 is applied as torque T to the load cell 26 via a wire, and the change is measured. It is read by the dynamic strain meter 27 and recorded by the recorder 28. When the seizure phenomenon occurs, the torque T increases rapidly. Therefore, the contact pressure acting on the sliding contact surface when the torque T rapidly increases is defined as the seizure-generating surface pressure, and the quality of the seizure characteristics is determined based on the magnitude of this seizure-generating surface pressure.
試験条件は次、の通りである。The test conditions are as follows.
摺動速度：８ｍ７ｓｅｃ
潤滑油５ＳＡＥ ＳＥ級 １０Ｗ−３０モータオイル
潤滑油供給条件：３００ｃｃ／ｍｉｎ
潤滑油温度二８０℃
接触圧カニ２０Ｋｇ／ｃｍ”から３分間経過毎に１０Ｋ
ｇ／ｃｍｆず
つ上昇させる。Sliding speed: 8m7sec Lubricating oil 5SAE SE class 10W-30 motor oil Lubricating oil supply conditions: 300cc/min Lubricating oil temperature 280℃ Contact pressure 10K every 3 minutes from 20Kg/cm''
Increase by g/cmf.
相手摺動部材（ステータ） ：鋳鉄材ＦＣ２０供試試料
：
試料１．（従来技術）−硬質クロムめっきを試験片２５
表面に５０μｍ付け、エメリ
ーペーパーで所定の表面粗さに調整し
たもの、めっき硬さはＨｖ９１０であ
試料２． （従来技術）−試験片２５（マルテンサイト
系１７Ｃｒステンレス材）をガ
ス窒化処理したのち、表面の酸化層及
び白層を取り除き、エメリーペーパー
で所定の表面粗さに調整したもの、窒
化層の厚さは９０μｍ１硬さはＨｖ１
２００である。Mating sliding member (stator): Cast iron FC20 test sample: Sample 1. (Prior art) - Hard chrome plating test piece 25
Sample 2 was coated with a thickness of 50 μm on the surface and adjusted to a specified surface roughness with emery paper, and the plating hardness was Hv910. (Prior art) - Test piece 25 (martensitic 17Cr stainless steel material) was subjected to gas nitriding treatment, the oxide layer and white layer on the surface were removed, and the surface roughness was adjusted to a specified level with emery paper. The thickness of the nitrided layer The thickness is 90 μm and the hardness is Hv1 200.
試料３．（従来技術）−試験片２５（マルテンサイト系
１７Ｃｒステンレス材）をガ
ス窒化処理したのち、表面の酸化層及
び白層を取り除き、エメリーペーパー
で所定の表面粗さに調整し、イオンブ
レーティングにより窒化チタン皮膜を
被覆したもの、イオンプレーティング
条件は試験１と同じである。窒化層の
厚さは９０．ｕｎ、硬さはＨｖＩ ２００、窒化チタン
皮膜の厚さは２．５μｍで、硬さはＨ，２５００である
。Sample 3. (Prior art) - After gas nitriding test piece 25 (martensitic 17Cr stainless steel material), the oxidized layer and white layer on the surface were removed, the surface roughness was adjusted to a specified level with emery paper, and nitrided by ion blasting. The titanium coating and ion plating conditions were the same as in Test 1. The thickness of the nitride layer is 90. The hardness is HvI 200, the thickness of the titanium nitride film is 2.5 μm, and the hardness is H2500.
試料４． （本発明）−試験片２５ （マルテンサイト
系１７Ｃｒステンレス材）をガス
窒化処理したのち、表面の酸化層及び
白層を取り除き、エメリーペーパーで
所定の表面粗さに調整し、イオンブレ
ーティングにより窒化チタン皮膜を被
覆したもの、ただし、被覆時の炉内圧
（窒素分圧）を随時変化させて、窒化
チタン皮膜層の靭性を表層に向かうに
従い徐々に低くし、表層部は窒素濃度
を高くし、脆くしたものである。イオ
ンブレーティングの条件は試験１と同
じである。窒化層の厚さは９０μｍ、
硬さはＨｖＩ ２００で、窒化チタン皮膜の表面硬さは
Ｈｖ２０００、厚さは
２．５μｍである。Sample 4. (Present invention) - After gas nitriding test piece 25 (martensitic 17Cr stainless steel material), the oxide layer and white layer on the surface were removed, the surface roughness was adjusted to a specified level with emery paper, and the surface was nitrided by ion blasting. Coated with titanium film, however, by changing the furnace pressure (nitrogen partial pressure) at the time of coating, the toughness of the titanium nitride film layer is gradually lowered toward the surface layer, and the nitrogen concentration is increased in the surface layer. It is made brittle. The ion blating conditions were the same as in Test 1. The thickness of the nitride layer is 90 μm and the hardness is HvI 200, and the surface hardness of the titanium nitride film is Hv2000 and the thickness is 2.5 μm.
試料５． （本発明）−試験片２５ （マルテンサイト
系１７Ｃｒステンレス材）をガス
窒化処理したのち、表面の酸化層及び
白層を取り除き、エメリーペーパーで
所定の表面粗さに調整し、イオンブレ
ーティングにより窒化チタン皮膜を被
覆したもの、ただし、被覆時の炉内圧
（窒素分圧）を随時変化させて、窒化
チタン皮膜層の窒素濃度を表層に向か
うに従い徐々に低くし、表層部の硬さ
をＨｖ１８００以下にしたものである
、イオンプレーティングの条件は試験
１と同じである。窒化層の厚さは９０
ｐｍ、硬さはＨｖ１２００で、窒化チ
タン皮膜の表面硬さはＨｖｌ ７５０、厚さは２．５μ
ｍである。Sample 5. (Present invention) - After gas nitriding test piece 25 (martensitic 17Cr stainless steel material), the oxide layer and white layer on the surface were removed, the surface roughness was adjusted to a specified level with emery paper, and the surface was nitrided by ion blasting. Titanium film coated, however, the furnace pressure (nitrogen partial pressure) at the time of coating is changed at any time to gradually lower the nitrogen concentration of the titanium nitride film layer toward the surface layer, and the hardness of the surface layer is reduced to Hv1800 or less. The ion plating conditions were the same as in Test 1. The thickness of the nitride layer is 90 pm and the hardness is Hv1200, and the surface hardness of the titanium nitride film is Hvl 750 and the thickness is 2.5μ.
It is m.
なお、各試料１〜５の表面粗さは全て０．８μｍＲｚで
ある。In addition, the surface roughness of each sample 1-5 is all 0.8 micrometerRz.
試験結果を第９図に示す。The test results are shown in Figure 9.
第９図に示す如く、本発明皮膜は従来技術の表面処理皮
膜に比べ、良好な耐焼き付き性を示した。As shown in FIG. 9, the film of the present invention exhibited better seizure resistance than the surface-treated film of the prior art.
これは本発明皮膜は初期馴染み性に優れているために、
試験初期において良好な摺動面が形成されるためと考え
られる。This is because the film of the present invention has excellent initial adaptability.
This is thought to be because a good sliding surface was formed in the initial stage of the test.
（試験３）
第１圧力リングの摺動面に下記に示す表面処理を施し、
エンジンテストに供した。シリンダブロックの材質はＦ
Ｃ２５相当材である。(Test 3) The sliding surface of the first pressure ring was subjected to the surface treatment shown below.
Subjected to engine test. The material of the cylinder block is F.
It is a material equivalent to C25.
試料１． （従来技術）−マルテンサイト系１７Ｃｒ
ステンレス製ピストンリングの全
表面にガス窒化処理したのち、表面の
酸化層及び白層を取り除いたもの、な
お、外周摺動面の窒化層の厚さは９０
μｍであり、硬さはＨｖｌ ２００である。Sample 1. (Prior art) - Martensitic 17Cr
After gas nitriding the entire surface of a stainless steel piston ring, the oxidized layer and white layer on the surface were removed.The thickness of the nitrided layer on the outer sliding surface is 90 μm, and the hardness is Hvl 200. be.
試料２． （従来技術）−マルテンサイト系１７Ｃｒス
テンレス製ピストンリングの全
表面にガス窒化処理したのち、表面の
酸化層及び白層を取り除き、パフ研磨
後イオンプレーティングにより、外周
摺動面に窒化チタン皮膜を被覆したも
の、イオンプレーティングの条件は試
験１と同じである。外周摺動面の窒化
層の厚さは９０μｍであり、硬さはＨ
ｖｌ２００である。窒化チタン皮膜の
厚さは４μｍであり、硬さはＨｖ２４
００である。Sample 2. (Prior art) - After gas nitriding the entire surface of a martensitic 17Cr stainless steel piston ring, the oxide layer and white layer on the surface are removed, and after polishing, a titanium nitride film is applied to the outer sliding surface by ion plating. The coating and ion plating conditions were the same as in Test 1. The thickness of the nitrided layer on the outer peripheral sliding surface is 90 μm, and the hardness is H vl200. The thickness of the titanium nitride film is 4 μm, and the hardness is Hv2400.
試料３． （本発明）−マルテンサイト系１７Ｃｒステ
ンレス製ピストンリングの全表
面にガス窒化処理したのち、表面の酸
化層及び白層を取り除き、パフ研磨後
イオンプレーティングにより、外周摺
動面に窒化チタン皮膜を被覆したもの
、ただし、被覆時の炉内圧（窒素分圧
）を随時変化させて、窒化チタン皮膜
層の靭性を表層に向かうに従い徐々に
低くし、表層部は窒素濃度を高くし、
脆くしたものである。イオンブレーテ
ィングの条件は試験１と同じである。Sample 3. (The present invention) - After gas nitriding the entire surface of a martensitic 17Cr stainless steel piston ring, the oxide layer and white layer on the surface are removed, and after puff polishing, a titanium nitride film is applied to the outer sliding surface by ion plating. However, by changing the furnace pressure (nitrogen partial pressure) at the time of coating, the toughness of the titanium nitride film layer is gradually lowered toward the surface layer, and the nitrogen concentration is increased in the surface layer, making it brittle. It is. The ion blating conditions were the same as in Test 1.
外周摺動面の窒化層の厚さは９０μｍ であり、硬さはＨｖｌ ２００である。The thickness of the nitride layer on the outer peripheral sliding surface is 90μm The hardness is Hvl 200.
窒化チタン皮膜の厚さは４μｍであり 、表面硬さはＨｖ２０００である。The thickness of the titanium nitride film is 4 μm. , the surface hardness is Hv2000.
試料４． （本発明）−マルテンサイト系１７Ｃｒステ
ンレス製ピストンリングの全表
面にガス窒化処理したのち、表面の酸
化層及び白層を取り除き、パフ研磨後
イオンプレーティングにより、外周摺
動面に窒化チタン皮膜を被覆したもの
、ただし、被覆時の炉内圧（窒素分圧
）を随時変化させて、窒化チタン皮膜
層の窒素濃度を表層に向かうに従い徐
々に低くし、表層部の硬さをＨｖ１８
００以下にしたものである。イオンブ
レーティングの条件は試験１と同じで
ある。外周摺動面の窒化層の厚さは９
０μｍであり、硬さはＨｖｌ ２００である。窒化チタ
ン皮膜の厚さは４μｍ
であり、表面硬さはＨｖｌ ７８０である。Sample 4. (The present invention) - After gas nitriding the entire surface of a martensitic 17Cr stainless steel piston ring, the oxide layer and white layer on the surface are removed, and after puff polishing, a titanium nitride film is applied to the outer sliding surface by ion plating. However, by changing the furnace pressure (nitrogen partial pressure) at the time of coating, the nitrogen concentration of the titanium nitride film layer was gradually lowered toward the surface layer, and the hardness of the surface layer was reduced to Hv1800 or less. It is something. The ion blating conditions were the same as in Test 1. The thickness of the nitrided layer on the outer peripheral sliding surface is 90 μm, and the hardness is Hvl 200. The thickness of the titanium nitride film is 4 μm, and the surface hardness is Hvl 780.
各試料１〜４の外周摺動面の表面粗さは全て０゜８μｍ
Ｒｚである。The surface roughness of the outer sliding surface of each sample 1 to 4 is all 0°8 μm.
It is Rz.
上記のピストンリングを排気量２０００ｃｃ、水冷６気
筒の４サイクルガソリンエンジンに組み込み、加鉛ガソ
リンを燃料として、回転数５２０Ｑｒｐｍ、水！１１０
℃、油温１３０℃以上、全負荷の条件で１０時間のスカ
ッフテストを２回実施した。テスト後のピストンリング
外周摺動面及びシリンダ内周面のスカッフィングの状況
は次の通りである。The above piston ring is installed in a 4-stroke gasoline engine with a displacement of 2000 cc and a water-cooled 6 cylinder, using leaded gasoline as fuel and rotating at a speed of 520 Qrpm. 110
℃, oil temperature of 130°C or higher, and a 10-hour scuff test was conducted twice under full load conditions. The status of scuffing on the outer peripheral sliding surface of the piston ring and the inner peripheral surface of the cylinder after the test is as follows.
試料１はスカッフィングが発生し、試料２はスカッフィ
ングの発生はないものの、傷の発生があり、試料３．４
はスカッフィング、傷の発生は認められなかった。Sample 1 had scuffing, sample 2 had no scuffing but scratches, and sample 3.4
No scuffing or scratches were observed.
以上のように、本発明品は、ピストンリング外周摺動面
はもちろんシリンダ内周面にもスカッフィングの発生は
全く認められず、また傷もなく、良好な初期馴染み性及
び耐焼付性を持つことが確認された。As described above, the product of the present invention shows no scuffing or scratches on the piston ring's outer sliding surface or the cylinder's inner peripheral surface, and has good initial fit and seizure resistance. confirmed.
（試験４）
試験３で作製したピストンリングを耐久テストに供試し
、耐摩耗性について調査した。(Test 4) The piston ring produced in Test 3 was subjected to a durability test, and its wear resistance was investigated.
各°ピストンリングを排気量２０００ｃｃ、水冷６気筒
の４サイクルガソリンエンジンに組み込み、無鉛ガソリ
ンを燃料として、回転数５２００ｒｐｍ、水温９０℃、
油温１１０℃、全負荷の条件で１００時間の耐久テスト
を実施した。Each °piston ring is installed in a 2000cc displacement, 6-cylinder water-cooled, 4-stroke gasoline engine, running on unleaded gasoline as fuel, rotating at 5200rpm, water temperature at 90℃,
A 100-hour durability test was conducted at an oil temperature of 110°C and full load.
第１０図にピストンリングの外周摺動面及びシリンダ内
周面のＴＯＰ−ＴＤＣ部の摩耗を示す。FIG. 10 shows the wear of the TOP-TDC portion of the outer peripheral sliding surface of the piston ring and the inner peripheral surface of the cylinder.
また、第１１図に１００時間運転後の第１圧力リングの
外周摺動面形状を示す、（Ａ）は試料１、（Ｂ）は試料
２、（Ｃ）は試料３、（Ｄ）は試料４のものである。In addition, Fig. 11 shows the shape of the outer peripheral sliding surface of the first pressure ring after 100 hours of operation. (A) is sample 1, (B) is sample 2, (C) is sample 3, and (D) is sample 4.
第１０図に示す如く、運転初期においては本発明品は、
従来技術によるピストンリングよりも自分自身の摩耗量
は多いものの、ピストンリングとシリンダとの合計摩耗
量は本発明品の方が少ない。As shown in Figure 10, at the initial stage of operation, the product of the present invention:
Although the piston ring itself wears more than the conventional piston ring, the total wear of the piston ring and cylinder is smaller in the product of the present invention.
１００時間運転後においては、ピストンリングの摩耗量
については本発明品と従来品との差がな（なり、シリン
ダの摩耗量については本発明品の方が摩耗が少ないこと
が確認された。After 100 hours of operation, there was no difference in the amount of wear of the piston rings between the product of the present invention and the conventional product (it was confirmed that the amount of wear of the cylinder of the present invention was less than that of the product of the present invention).
また、第１１図に示す如く、本発明ピストンリングの外
周摺動面形状は運転初期において良好な摺動面形状が形
成される。このことが運転初期以降の耐摩耗性能に大き
な影響を与えたものと考えられる０面圧が低下したのち
は従来技術による窒化チタン皮膜と同等の膜が表面に出
て来るために耐摩耗性があるものと考えられる。Further, as shown in FIG. 11, the outer peripheral sliding surface of the piston ring of the present invention has a good sliding surface shape at the initial stage of operation. This is thought to have had a major impact on the wear resistance performance after the initial stage of operation.After the zero surface pressure decreases, a film equivalent to the titanium nitride film produced by the conventional technology appears on the surface, which improves the wear resistance. It is thought that there is.
以上説明したように、本発明のピストンリングは耐摩耗
性、耐焼付性に優れ、且つ初期馴染み性に優れた効果を
有するものである。As explained above, the piston ring of the present invention has excellent wear resistance, seizure resistance, and excellent initial fit.
第１図及び第２図は本発明ピストンリングの断面図、第
３図は窒化処理層の温度による硬さの変化を示す図、第
４図は往復動摩擦試験機の説明図、第５図（Ａ）は上試
験片の摩耗量算出説明図、第５図（Ｂ）は下試験片の摩
耗量算出説明図、第６図は試験１の試験結果を示す図、
第７図及び第８図はビン・ディスク型高面圧摩擦試験機
の説明図、第９図は試験２の試験結果を示す図、第１０
図は試験３の試験結果を示す図、第１１図は試験４の試
験結果を示す図で（Ａ）は試料ｌ、（Ｂ）は試料２、（
Ｃ）は試料３、（Ｄ）は試料４のものである。
第１図
第２図
第３図
熱
荊 温度（０Ｃ）
第５図
（Ｂ）
第７図
第９図
第１０図
第１１図Figures 1 and 2 are cross-sectional views of the piston ring of the present invention, Figure 3 is a diagram showing changes in hardness due to temperature of the nitrided layer, Figure 4 is an explanatory diagram of a reciprocating friction tester, and Figure 5 ( A) is an explanatory diagram for calculating the amount of wear on the upper test piece, FIG. 5 (B) is an explanatory diagram for calculating the amount of wear on the lower test piece, and FIG. 6 is a diagram showing the test results of Test 1.
Figures 7 and 8 are explanatory diagrams of the bottle-disc type high surface pressure friction tester, Figure 9 is a diagram showing the test results of Test 2, and Figure 10 is a diagram showing the test results of Test 2.
The figure shows the test results of Test 3, and FIG. 11 shows the test results of Test 4. (A) is sample 1, (B) is sample 2, (
C) is sample 3, and (D) is sample 4. Figure 1 Figure 2 Figure 3 Heat temperature (0C) Figure 5 (B) Figure 7 Figure 9 Figure 10 Figure 11
Claims (6)
たピストンリングにおいて、少なくとも外周摺動面の窒
化チタン皮膜層の靭性を表層に向かうに従い徐々に低く
し、表層部は窒素濃度を高くして詭くしたことを特徴と
するピストンリング。(1) In a piston ring with a titanium nitride film formed on at least the outer sliding surface, the toughness of the titanium nitride film layer on at least the outer sliding surface is gradually lowered toward the surface layer, and the nitrogen concentration is increased in the surface layer. A piston ring characterized by sophistication.
たピストンリングにおいて、少なくとも外周摺動面の窒
化チタン皮膜層の窒素濃度を表層に向かうに従い徐々に
低くし、表層部の硬さをＨｖ１８００以下にしたことを
特徴とするピストンリング。(2) In a piston ring with a titanium nitride film formed on at least the outer sliding surface, the nitrogen concentration of the titanium nitride film layer on at least the outer sliding surface is gradually lowered toward the surface layer, and the hardness of the surface layer is lower than Hv1800. A piston ring characterized by:
化層上に窒化チタン皮膜を形成したピストンリングにお
いて、少なくとも外周摺動面の窒化チタン皮膜層の靭性
を表層に向かうに従い徐々に低くし、表層部は窒素濃度
を高くして脆くしたことを特徴とするピストンリング。(3) In a piston ring in which a nitride layer is formed on at least the outer peripheral sliding surface and a titanium nitride film is formed on the nitrided layer, the toughness of the titanium nitride film layer on at least the outer peripheral sliding surface is gradually lowered toward the surface layer. A piston ring characterized by having a high nitrogen concentration in the surface layer to make it brittle.
化層上に窒化チタン皮膜を形成したピストンリングにお
いて、少なくとも外周摺動面の窒化チタン皮膜層の窒素
濃度を表層に向かうに従い徐々に低くし、表層部の硬さ
をＨｖ１８００以下にしたことを特徴とするピストンリ
ング。(4) In a piston ring in which a nitrided layer is formed on at least the outer sliding surface and a titanium nitride film is formed on the nitrided layer, the nitrogen concentration of the titanium nitride film layer on at least the outer peripheral sliding surface is gradually reduced toward the surface layer. A piston ring characterized by having a lower surface layer hardness of Hv1800 or less.
あることを特徴とする請求項３又は４記載のピストンリ
ング。(5) The piston ring according to claim 3 or 4, wherein the nitrided layer is a layer from which a surface oxidation layer and a white layer have been removed.
グによることを特徴とする請求項１、２、３、４又は５
記載のピストンリング。(6) Claim 1, 2, 3, 4 or 5, wherein the titanium nitride film is coated by ion plating.
Piston rings listed.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63314347A JP2649835B2 (en) | 1988-12-13 | 1988-12-13 | piston ring |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63314347A JP2649835B2 (en) | 1988-12-13 | 1988-12-13 | piston ring |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH02159478A true JPH02159478A (en) | 1990-06-19 |
| JP2649835B2 JP2649835B2 (en) | 1997-09-03 |
Family
ID=18052233
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP63314347A Expired - Fee Related JP2649835B2 (en) | 1988-12-13 | 1988-12-13 | piston ring |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2649835B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0298262U (en) * | 1989-01-23 | 1990-08-06 | ||
| US20110244266A1 (en) * | 2008-12-17 | 2011-10-06 | Sumitomo Metal Industries, Ltd. | Titanium material and method for producing titanium material |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6113064A (en) * | 1984-06-28 | 1986-01-21 | Teikoku Piston Ring Co Ltd | Piston ring for internal-combustion engine |
| JPS62188856A (en) * | 1986-02-13 | 1987-08-18 | Riken Corp | Piston ring |
| JPH02129467A (en) * | 1988-11-08 | 1990-05-17 | Toyota Motor Corp | Piston ring and manufacture thereof |
-
1988
- 1988-12-13 JP JP63314347A patent/JP2649835B2/en not_active Expired - Fee Related
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6113064A (en) * | 1984-06-28 | 1986-01-21 | Teikoku Piston Ring Co Ltd | Piston ring for internal-combustion engine |
| JPS62188856A (en) * | 1986-02-13 | 1987-08-18 | Riken Corp | Piston ring |
| JPH02129467A (en) * | 1988-11-08 | 1990-05-17 | Toyota Motor Corp | Piston ring and manufacture thereof |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0298262U (en) * | 1989-01-23 | 1990-08-06 | ||
| US20110244266A1 (en) * | 2008-12-17 | 2011-10-06 | Sumitomo Metal Industries, Ltd. | Titanium material and method for producing titanium material |
| US9487882B2 (en) * | 2008-12-17 | 2016-11-08 | Nippon Steel & Sumitomo Metal Corporation | Titanium material and method for producing titanium material |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2649835B2 (en) | 1997-09-03 |
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