JP5763260B2 - Wire for pressure ring and manufacturing method thereof - Google Patents
Wire for pressure ring and manufacturing method thereof Download PDFInfo
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- JP5763260B2 JP5763260B2 JP2014262736A JP2014262736A JP5763260B2 JP 5763260 B2 JP5763260 B2 JP 5763260B2 JP 2014262736 A JP2014262736 A JP 2014262736A JP 2014262736 A JP2014262736 A JP 2014262736A JP 5763260 B2 JP5763260 B2 JP 5763260B2
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- 238000004519 manufacturing process Methods 0.000 title claims description 17
- 229910001567 cementite Inorganic materials 0.000 claims description 30
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 claims description 30
- 239000002245 particle Substances 0.000 claims description 17
- 238000011282 treatment Methods 0.000 claims description 17
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 12
- 238000000137 annealing Methods 0.000 claims description 12
- 238000005496 tempering Methods 0.000 claims description 11
- 239000011159 matrix material Substances 0.000 claims description 9
- 229910052742 iron Inorganic materials 0.000 claims description 6
- 238000010791 quenching Methods 0.000 claims description 6
- 230000000171 quenching effect Effects 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 5
- 239000006185 dispersion Substances 0.000 claims description 4
- 238000000465 moulding Methods 0.000 claims description 2
- 241000428199 Mustelinae Species 0.000 claims 2
- 229910000831 Steel Inorganic materials 0.000 description 24
- 230000000052 comparative effect Effects 0.000 description 24
- 239000000463 material Substances 0.000 description 24
- 239000010959 steel Substances 0.000 description 24
- 239000003921 oil Substances 0.000 description 18
- 229910052782 aluminium Inorganic materials 0.000 description 15
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 15
- 238000000034 method Methods 0.000 description 15
- 230000008569 process Effects 0.000 description 12
- 238000012360 testing method Methods 0.000 description 11
- 238000010438 heat treatment Methods 0.000 description 9
- 101100043866 Caenorhabditis elegans sup-10 gene Proteins 0.000 description 8
- 239000011248 coating agent Substances 0.000 description 8
- 238000000576 coating method Methods 0.000 description 8
- 229910000734 martensite Inorganic materials 0.000 description 8
- 239000000203 mixture Substances 0.000 description 7
- 229910008458 Si—Cr Inorganic materials 0.000 description 5
- 229910052799 carbon Inorganic materials 0.000 description 5
- 230000006835 compression Effects 0.000 description 5
- 238000007906 compression Methods 0.000 description 5
- 239000011572 manganese Substances 0.000 description 5
- 238000012545 processing Methods 0.000 description 5
- 238000004381 surface treatment Methods 0.000 description 5
- 229910045601 alloy Inorganic materials 0.000 description 4
- 239000000956 alloy Substances 0.000 description 4
- 238000005275 alloying Methods 0.000 description 4
- 238000002485 combustion reaction Methods 0.000 description 4
- CPSYWNLKRDURMG-UHFFFAOYSA-L hydron;manganese(2+);phosphate Chemical compound [Mn+2].OP([O-])([O-])=O CPSYWNLKRDURMG-UHFFFAOYSA-L 0.000 description 4
- 238000005491 wire drawing Methods 0.000 description 4
- 230000007423 decrease Effects 0.000 description 3
- 230000002093 peripheral effect Effects 0.000 description 3
- 230000009467 reduction Effects 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- LRXTYHSAJDENHV-UHFFFAOYSA-H zinc phosphate Chemical compound [Zn+2].[Zn+2].[Zn+2].[O-]P([O-])([O-])=O.[O-]P([O-])([O-])=O LRXTYHSAJDENHV-UHFFFAOYSA-H 0.000 description 3
- 229910000165 zinc phosphate Inorganic materials 0.000 description 3
- 239000002585 base Substances 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 238000010191 image analysis Methods 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 238000007733 ion plating Methods 0.000 description 2
- 238000007747 plating Methods 0.000 description 2
- 238000012546 transfer Methods 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910001018 Cast iron Inorganic materials 0.000 description 1
- 229910017112 Fe—C Inorganic materials 0.000 description 1
- 229910000639 Spring steel Inorganic materials 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000002860 competitive effect Effects 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 239000012458 free base Substances 0.000 description 1
- 239000003574 free electron Substances 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000005121 nitriding Methods 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 238000010587 phase diagram Methods 0.000 description 1
- 238000005240 physical vapour deposition Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 230000004044 response Effects 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
- 239000002335 surface treatment layer Substances 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
Landscapes
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
- Pistons, Piston Rings, And Cylinders (AREA)
Description
本発明は、自動車エンジン用ピストンリング用線材に関し、特に高圧縮比のエンジンの熱負荷の高い環境に晒される圧力リングに使用される圧力リング用線材及びその製造方法に関する。 The present invention relates to a wire for a piston ring for an automobile engine, and more particularly, to a wire for a pressure ring used for a pressure ring exposed to an environment with a high heat load of a high compression ratio engine and a method for manufacturing the wire.
近年、自動車エンジンは、環境対応のため、燃費の向上、低エミッション化、高出力化が図られ、エンジン仕様は、高圧縮比化、高負荷化の傾向にある。ところが、一般に圧縮比を高くすると、燃焼室温度も高くなりノッキングが発生し易くなる。通常のノッキング対策は点火時期（進角）を遅らせることで対応されているが、それでは高い熱効率を維持できないため、燃焼室壁温度を下げる方向の検討も行われている。燃焼室壁温度の低下には、ピストン冠面温度を下げることが有効で、それにはピストンの熱を冷却されたシリンダー壁へ圧力リングを経て逃れさせることが最も効果的である。すなわち、ピストンリングの三つの基本機能であるガスシール機能、熱伝導機能、オイルコントロール機能のうちの熱伝導機能を利用することになる。熱伝導機能は、母材や表面処理層の熱伝導率、形状等に密接に関係するので、これらを最適化すれば良い一方、材料の選定にあたっては、熱伝導率の他に、約300℃程度の熱的環境に晒されてもリング特性を維持できる耐熱ヘタリ性や疲労強度も要求される。 In recent years, automobile engines have been improved in fuel efficiency, low emission, and high output in order to cope with the environment, and engine specifications tend to have high compression ratios and high loads. However, generally, when the compression ratio is increased, the temperature of the combustion chamber is also increased and knocking is likely to occur. Ordinary knocking countermeasures are dealt with by delaying the ignition timing (advance angle). However, since this cannot maintain high thermal efficiency, studies are also being made to lower the combustion chamber wall temperature. In order to lower the combustion chamber wall temperature, it is effective to lower the piston crown surface temperature, and it is most effective to let the heat of the piston escape to the cooled cylinder wall through the pressure ring. That is, the heat transfer function among the three basic functions of the piston ring, that is, the gas seal function, the heat transfer function, and the oil control function is used. The heat conduction function is closely related to the thermal conductivity, shape, etc. of the base material and the surface treatment layer, so these can be optimized. Heat resistance and fatigue strength that can maintain the ring characteristics even when exposed to a certain degree of thermal environment are also required.
また、ピストンがアルミニウム（以下「アルミ」という。）製の場合、燃焼室温度の上昇に伴いアルミが軟化し、ピストンのリング溝内で、圧力リングによる高温での叩きと摺動により疲労破壊を起こし、リング溝摩耗や圧力リングへのアルミ凝着が発生しやすくなる。この点からも熱伝導の高い圧力リングを用いてリング溝温度を下げることが要求される。 In addition, when the piston is made of aluminum (hereinafter referred to as “aluminum”), the aluminum softens as the temperature of the combustion chamber rises, and fatigue damage occurs due to high-temperature striking and sliding in the piston ring groove. As a result, ring groove wear and aluminum adhesion to the pressure ring are likely to occur. Also from this point, it is required to lower the ring groove temperature by using a pressure ring having high heat conduction.
上記のような要求に対して、例えば特許文献１には、熱伝導性と耐熱ヘタリ性に優れ、圧力リングとして適用可能なピストンリングとして、C、Si、Mn、Crの適正成分範囲を所定のパラメータに規定したピストンリング組成が提案されている。 In response to the above requirements, for example, Patent Document 1 discloses a predetermined component range of C, Si, Mn, and Cr as a piston ring that is excellent in thermal conductivity and heat resistance and can be applied as a pressure ring. Piston ring compositions specified in the parameters have been proposed.
しかしながら、例えば、熱伝導率が35 W/m・K以上、熱ヘタリ率（リングの接線張力減退度）が4％以下を目標とすれば、その目標を達成するのは困難な状況にある。 However, for example, if the target is a thermal conductivity of 35 W / m · K or higher and a thermal settling rate (ring tangential tension reduction) of 4% or less, it is difficult to achieve the target.
さらに、ピストンリングのような自動車部品では、優れた特性だけでなく、競争力のある価格も要求されている。すなわち、いかにコストを低減できるかも重要な課題である。 Furthermore, automobile parts such as piston rings are required not only to have excellent characteristics but also to have a competitive price. In other words, how to reduce costs is an important issue.
本発明は、高圧縮比のエンジンの熱負荷の高い環境で使用することが可能な、熱伝導性と耐熱ヘタリ性に優れ、且つ価格競争力のある圧力リングの製造に使用される圧力リング用線材を提供することを課題とする。また、上記圧力リング用線材の製造方法を提供することを課題とする。 INDUSTRIAL APPLICABILITY The present invention is for a pressure ring that can be used in a high compression ratio engine in an environment with a high thermal load, and that is excellent in thermal conductivity and heat resistance, and used for manufacturing a cost-competitive pressure ring. An object is to provide a wire rod. It is another object of the present invention to provide a method for producing the pressure ring wire.
表１に、ピストンリングに使用されている鋼材A〜Gの組成と200℃における熱伝導率を示す。各鋼材の熱伝導率と合金元素の組成和との関係を整理すると図６のようになる。すなわち、合金元素量が少ない材料ほど熱伝導率が高い。 Table 1 shows the compositions of steel materials A to G used in the piston ring and the thermal conductivity at 200 ° C. FIG. 6 shows the relationship between the thermal conductivity of each steel material and the composition sum of the alloy elements. That is, a material having a smaller alloy element amount has a higher thermal conductivity.
しかし、実際には、合金元素量が少なくなると、耐熱ヘタリ性に劣り、熱負荷の高い環境では圧力リングとしての使用に供せなくなる。また、鋼材のコストは、一般に合金元素量が少ないほど安価であるが、それに加えて、市場経済の観点からは、市場で使用されている量が多いほど、すなわち、JIS（日本工業規格）登録材料のように大量生産されている鋼材ほど安価である。よって、本発明では、基本的には合金元素量の少ないJIS登録材料を使用するが、300℃の高温でも優れた耐熱ヘタリ性を発揮するように顕微鏡組織を調製することとする。本発明者は、鋭意研究の結果、具体的には、JIS G 4801に規定される材料記号SUP10なる鋼材を用い、ピストンリング線材をオイルテンパー処理する前に、焼鈍し、球状化セメンタイトを析出させ、かつオイルテンパー処理条件を最適化することにより焼戻マルテンサイトマトリックス中に球状化セメンタイトを適量分散させ、300℃においても転位の移動やクリープを抑制し、耐熱ヘタリ性を向上させることができることに想到した。 However, in practice, if the amount of alloying elements is reduced, the heat resistance is inferior and cannot be used as a pressure ring in an environment with a high heat load. In addition, the cost of steel is generally lower as the amount of alloying elements is smaller. In addition, from the viewpoint of market economy, the more used the steel, the more JIS (Japanese Industrial Standard) registered. Steel materials that are mass-produced like materials are less expensive. Therefore, in the present invention, a JIS registered material having a small amount of alloying element is basically used, but the microstructure is prepared so as to exhibit excellent heat-resistant settling properties even at a high temperature of 300 ° C. As a result of diligent research, the present inventor, specifically, using a steel material with the material symbol SUP10 defined in JIS G 4801, annealed the piston ring wire before oil temper treatment to precipitate spheroidized cementite. In addition, by optimizing the oil temper treatment conditions, it is possible to disperse an appropriate amount of spheroidized cementite in the tempered martensite matrix, suppress dislocation movement and creep even at 300 ° C., and improve heat resistance. I came up with it.
すなわち、本発明の圧力リング用線材は、質量％で、C：0.45〜0.55、Si：0.15〜0.35、Mn：0.65〜0.95、Cr：0.80〜1.10、V：0.15〜0.25、残部が鉄及び不可避的不純物からなる組成を有し、焼戻マルテンサイトマトリックス中に平均粒径0.1〜1.5μmの球状化セメンタイトが分散し、熱伝導率が35 W/m・K以上、熱ヘタリ率が4.4％以下である圧力リングの製造に使用されることを特徴とする。球状化セメンタイトは平均粒径0.5〜1.0μmが好ましい。また、球状化セメンタイトの分散量は、顕微鏡組織観察面において、1〜6面積％とすることが好ましい。 That is, the wire for a pressure ring of the present invention is in mass%, C: 0.45-0.55, Si: 0.15-0.35, Mn: 0.65-0.95, Cr: 0.80-1.10, V: 0.15-0.25, the balance being iron and inevitable Spheroidized cementite with an average particle size of 0.1 to 1.5 μm dispersed in a tempered martensite matrix, thermal conductivity of 35 W / m · K or more, and thermal sag ratio of 4.4% or less It is used for manufacture of the pressure ring which is. The spheroidized cementite preferably has an average particle size of 0.5 to 1.0 μm. Further, the dispersion amount of the spheroidized cementite is preferably 1 to 6% by area on the microscope structure observation surface.
さらに、本発明の圧力リング用線材は、熱伝導率が38 W/m・K以上、熱ヘタリ率（リングの接線張力減退度）が4％以下である圧力リングの製造に使用されることが好ましい。 Furthermore, the wire for a pressure ring of the present invention may be used for manufacturing a pressure ring having a thermal conductivity of 38 W / m · K or more and a thermal settling rate (degree of tangential tension reduction of the ring) of 4% or less. preferable.
また、本発明の圧力リング用線材の製造方法は、質量％で、C：0.45〜0.55、Si：0.15〜0.35、Mn：0.65〜0.95、Cr：0.80〜1.10、V：0.15〜0.25、残部が鉄及び不可避的不純物からなる組成を有し、焼戻しマルテンサイトマトリックス中に平均粒径0.1〜1.5μmの球状化セメンタイトが分散している圧力リング用線材を製造する方法であって、圧力リング成形前のオイルテンパー処理工程以前に球状化セメンタイトを形成するための球状化焼鈍を含むことを特徴とする。球状化焼鈍は、温度600〜720℃で行われることが好ましく、オイルテンパー処理工程は、焼入温度820〜980℃、焼戻温度400〜500℃で行われることが好ましい。 Moreover, the manufacturing method of the wire for pressure rings of this invention is the mass%, C: 0.45-0.55, Si: 0.15-0.35, Mn: 0.65-0.95, Cr: 0.80-1.10, V: 0.15-0.25, remainder is A method for producing a wire for a pressure ring having a composition composed of iron and inevitable impurities, in which spheroidized cementite having an average particle size of 0.1 to 1.5 μm is dispersed in a tempered martensite matrix, before pressure ring molding And spheroidizing annealing for forming spheroidized cementite before the oil tempering step. The spheroidizing annealing is preferably performed at a temperature of 600 to 720 ° C, and the oil tempering step is preferably performed at a quenching temperature of 820 to 980 ° C and a tempering temperature of 400 to 500 ° C.
本発明の圧力リング用線材を用いて製造した圧力リングは、高熱伝導率と高い耐熱ヘタリ性を両立させており、高圧縮比エンジンのような熱負荷の高い環境での使用においても、リングの張力を減退させることなくピストンヘッドの熱を効率良く冷却されたシリンダー壁に逃すことができるため、点火時期を遅らすような調整をすることなくノッキングを抑制でき、高熱効率を維持できる。また同様に、アルミピストンのリング溝の温度を下げることもでき、アルミ凝着やリング溝摩耗を抑制することができる。さらに、本発明の製造方法によれば、JISに規定され大量生産されている鋼材を使用しているので、コストを低減することができる。 The pressure ring manufactured using the wire for a pressure ring of the present invention has both high thermal conductivity and high heat resistance, and even when used in an environment with a high heat load such as a high compression ratio engine, Since the heat of the piston head can be efficiently released to the cooled cylinder wall without reducing the tension, knocking can be suppressed without adjusting the ignition timing and high thermal efficiency can be maintained. Similarly, the temperature of the ring groove of the aluminum piston can be lowered, and aluminum adhesion and ring groove wear can be suppressed. Furthermore, according to the manufacturing method of the present invention, since the steel material specified in JIS and mass-produced is used, the cost can be reduced.
本発明の圧力リング用線材は、質量％で、C：0.45〜0.55、Si：0.15〜0.35、Mn：0.65〜0.95、Cr：0.80〜1.10、V：0.15〜0.25、残部が鉄及び不可避的不純物からなる組成を有し、焼戻マルテンサイトマトリックス中に平均粒径0.1〜1.5μmの球状化セメンタイトが分散している。上記組成は、基本的に、JIS G 4801に規定される材料記号SUP10の鋼材組成であり、CrとVを僅かに含むが合金元素の総量が少ないため、熱伝導率が高い。しかし、耐熱ヘタリ性は充分ではない。本発明では、比較的大きな球状化したセメンタイトを焼戻マルテンサイトマトリックス中に分散する。この球状化セメンタイトは、オイルテンパー処理するバネ鋼では残留セメンタイトとして知られており、応力集中源にもなるため、鋼線の機械的性質を低下させる要因として見られているものであるが、ピストンリングの圧力リングに使用した場合、優れた耐熱ヘタリ性を実現している事実からは、オイルテンパー後のマトリックス中に残った球状化セメンタイトの存在によって、結晶格子の歪みをつくるため、300℃でも転位を動きにくくするものと推量できる。本発明において、球状化セメンタイトは平均粒径0.1μm以上である。0.1μm程度以下の残留セメンタイトは、オイルテンパー処理の溶体化処理においてオーステナイト中に溶け込むため、平均粒径0.1μm未満の球状化セメンタイトとしては観測されない。また平均粒径が1.5μmを超えると疲労破壊の起源となって疲労強度を低減するので好ましくない。好ましくは平均粒径0.5〜1.0μmとする。 The wire for pressure ring of the present invention is mass%, C: 0.45-0.55, Si: 0.15-0.35, Mn: 0.65-0.95, Cr: 0.80-1.10, V: 0.15-0.25, the balance being iron and inevitable impurities The spheroidized cementite having an average particle size of 0.1 to 1.5 μm is dispersed in the tempered martensite matrix. The above composition is basically a steel material composition of the material symbol SUP10 defined in JIS G 4801, and contains a small amount of Cr and V but has a small total amount of alloy elements, so that the thermal conductivity is high. However, the heat resistance is not sufficient. In the present invention, relatively large spheroidized cementite is dispersed in a tempered martensite matrix. This spheroidized cementite is known as residual cementite in spring steel treated with oil temper, and is also a source of stress concentration, so it is seen as a factor that degrades the mechanical properties of steel wires. From the fact that when used for the pressure ring of the ring, excellent heat resistance is achieved, the presence of spheroidized cementite remaining in the matrix after oil tempering creates distortion of the crystal lattice, so even at 300 ° C It can be inferred that dislocation is difficult to move. In the present invention, the spheroidized cementite has an average particle size of 0.1 μm or more. Residual cementite of about 0.1 μm or less is not observed as spheroidized cementite having an average particle size of less than 0.1 μm because it dissolves into austenite in the solution treatment of oil temper treatment. On the other hand, if the average particle diameter exceeds 1.5 μm, it is not preferable because it causes fatigue fracture and reduces fatigue strength. The average particle diameter is preferably 0.5 to 1.0 μm.
また、球状化セメンタイトの分散量は、顕微鏡組織観察面において、1〜6面積％とすることが好ましい。さらにこの範囲の分散量であれば、熱伝導率が35 W/m・K以上となり、熱ヘタリ率（JIS B 8032-5に基づく接線張力減退度）も4％以下となり好ましい。通常使用されているSi-Cr鋼の熱伝導率は31 W/m・K程度であり、35 W/m・K程度の熱伝導率は、優れた熱伝導率を示す従来の片状黒鉛鋳鉄ピストンリングの熱伝導率に匹敵する。金属においては、熱伝導率は主に結晶粒内の自由電子の運動に支配されるため、固溶元素の少ないほど熱伝導率は向上する。本発明に使用するSUP10は、Si-Cr鋼に比べて固溶強化元素であるSiが特に少ないこと、また球状化セメンタイトを形成することも固溶Cを低減して熱伝導率の向上につながると考えられる。また、熱ヘタリ率は、JIS B 8032-5では、スチールリングの場合300℃×3時間の試験条件で接線張力減退度8％以下と規定されているが、小さければ小さいほど好ましく、材料開発における目標値としてSi-Cr鋼と同レベルの4％程度とした。 Further, the dispersion amount of the spheroidized cementite is preferably 1 to 6% by area on the microscope structure observation surface. Further, if the amount of dispersion is within this range, the thermal conductivity is preferably 35 W / m · K or more, and the thermal settling rate (degree of tangential tension reduction based on JIS B 8032-5) is preferably 4% or less. Conventionally used Si-Cr steel has a thermal conductivity of about 31 W / m · K, and a thermal conductivity of about 35 W / m · K is a conventional flake graphite cast iron that exhibits excellent thermal conductivity. Comparable to the thermal conductivity of the piston ring. In metals, the thermal conductivity is mainly governed by the movement of free electrons in the crystal grains, so the smaller the solid solution element, the higher the thermal conductivity. SUP10 used in the present invention has a particularly small amount of Si as a solid solution strengthening element compared to Si-Cr steel, and the formation of spheroidized cementite also reduces solid solution C and leads to an improvement in thermal conductivity. it is conceivable that. In addition, in JIS B 8032-5, the thermal sag rate is defined as a tangential tension decrease rate of 8% or less under the test conditions of 300 ° C x 3 hours in the case of steel rings. The target value was about 4%, the same level as Si-Cr steel.
鋼製圧力リングは、通常、耐摩耗性、耐スカッフ性の観点から、外周摺動面には様々な表面処理が行われている。熱伝導率が優先されるならCrめっきが好ましいが、耐摩耗性、耐スカッフ性を重視するならイオンプレーティングによるCrN皮膜、アルミシリンダーにはDLC皮膜が適しており、同じ圧力リングでも摺動相手材や使用環境等によって適した表面処理を選択することができる。もちろん、窒化処理も含まれる。 The steel pressure ring is usually subjected to various surface treatments on the outer peripheral sliding surface from the viewpoint of wear resistance and scuff resistance. Cr plating is preferable if thermal conductivity is a priority. However, if wear resistance and scuff resistance are important, CrN coating by ion plating and DLC coating are suitable for aluminum cylinders. A suitable surface treatment can be selected depending on the material and the use environment. Of course, nitriding is also included.
圧力リングの製造に使用される本発明の線材は、質量％で、C：0.45〜0.55、Si：0.15〜0.35、Mn：0.65〜0.95、Cr：0.80〜1.10、V：0.15〜0.25、残部が鉄及び不可避的不純物からなる組成の鋼材（SUP10）を溶製後、熱間圧延により線材とし、線材から通常はパテンチング−酸洗−伸線−パテンチング−酸洗−伸線−オイルテンパー（オイル焼入−焼戻）からなる一連の処理を経て所定の断面形状の線材としているところ、一部のパテンチングの処理の代わりに球状化焼鈍を行うことにより調製される。パテンチング処理とは、ライン熱処理において連続的に恒温変態又は冷却変態させて微細なパーライト組織にする熱処理法であり、具体的にはほぼ900から600℃の温度範囲で行われる。また、本発明において、このパテンチング処理の代わりに行われる球状化焼鈍は、Fe-C状態図のAC1点以下の温度600〜720℃の温度で30〜240分間行うのが好ましい。球状化焼鈍によって形成された所定の粒径の球状化セメンタイトは、その後の熱処理の影響を受け、またその後の伸線に影響するため、最後のオイルテンパー処理の直前に行うことが好ましい。従って、二回目のパテンチング処理の代わりに球状化焼鈍を行うことが好ましいが、その場合、球状化焼鈍はバッチ処理にせざるを得ず、すなわち従来の製造ラインの連続処理の途中にバッチ処理を挟むことになり生産性を落とさざるを得ない。生産性を優先し、一回目のパテンチング処理の代わりに行ってもよいが、球状化セメンタイトの粒径が所定の範囲にはいるよう注意が必要である。オイルテンパー処理は、いわゆる油焼入−焼戻処理であるが、球状化炭化物が全て溶け込まないような、すなわち好ましい面積率となるような温度と時間に設定する必要がある。本発明では、焼入工程は820〜980℃の温度で数十秒〜数分（例えば、30秒〜3分）の加熱をした後に行い、焼戻工程は、400〜500℃の温度で数十秒〜数分（例えば、30秒〜3分）程度行うのが好ましい。各熱処理温度と時間については、熱処理炉のサイズ、処理物の断面積により異なるため、球状化セメンタイトの粒径、面積率が好ましい範囲にはいるよう適宜調整する必要がある。 The wire rod of the present invention used for manufacturing the pressure ring is in mass%, C: 0.45-0.55, Si: 0.15-0.35, Mn: 0.65-0.95, Cr: 0.80-1.10, V: 0.15-0.25, the balance being After steel material (SUP10) composed of iron and inevitable impurities is melted, it is made into a wire rod by hot rolling. From the wire rod, it is usually patented, pickled, drawn, patented, pickled, drawn, oil temper (oil tempered) It is prepared by performing spheroidizing annealing instead of a part of the patenting process, after a wire having a predetermined cross-sectional shape is obtained through a series of processes consisting of tempering and tempering. The patenting treatment is a heat treatment method in which a constant tempering transformation or cooling transformation is performed continuously in a line heat treatment to form a fine pearlite structure, and is specifically performed in a temperature range of approximately 900 to 600 ° C. Further, in the present invention, spheroidizing annealing to be executed instead of the patenting process is preferably carried out at a temperature of Fe-C phase diagram of the A C1 point temperature below six hundred to seven hundred and twenty ° C. 30 to 240 minutes. Since the spheroidized cementite having a predetermined particle diameter formed by spheroidizing annealing is affected by the subsequent heat treatment and affects the subsequent wire drawing, it is preferably performed immediately before the final oil temper treatment. Therefore, it is preferable to perform spheroidizing annealing instead of the second patenting process, but in that case, spheroidizing annealing must be batch processing, that is, the batch processing is sandwiched in the middle of the continuous processing of the conventional production line. In other words, productivity has to be reduced. Although priority may be given to productivity, it may be performed instead of the first patenting treatment, but care must be taken that the particle size of the spheroidized cementite is within a predetermined range. The oil temper treatment is a so-called oil quenching-tempering treatment, but it is necessary to set the temperature and time so that all of the spheroidized carbides are not dissolved, that is, a preferable area ratio is obtained. In the present invention, the quenching process is performed after heating for several tens of seconds to several minutes (for example, 30 seconds to 3 minutes) at a temperature of 820 to 980 ° C., and the tempering process is performed at a temperature of 400 to 500 ° C. It is preferable to carry out for about 10 seconds to several minutes (for example, 30 seconds to 3 minutes). About each heat processing temperature and time, since it changes with the size of the heat processing furnace, and the cross-sectional area of a processed material, it is necessary to adjust suitably so that the particle size and area ratio of spheroidized cementite may fall in a preferable range.
圧力リングは、所定の断面形状に伸線された本発明の上記線材から、通常はカム成形機を用いてリングの自由形状に成形され、歪取り熱処理を行い、側面、外周、合口等を研削し、所定のリング形状に加工して得られる。もちろん、必要に応じて、めっきやPVD等の表面処理が施される。 The pressure ring is formed from the above-mentioned wire rod of the present invention drawn into a predetermined cross-sectional shape into a free shape of the ring, usually using a cam forming machine, and subjected to strain relief heat treatment to grind the side, outer periphery, joint, etc. And processed into a predetermined ring shape. Of course, surface treatment such as plating or PVD is performed as necessary.
実施例１〜３（J1〜J3）
直径8 mmφに圧延したSUP10鋼材から、加熱（900℃）−パテンチング（600℃）−酸洗−伸線−加熱（900℃）−パテンチング（600℃）−酸洗−伸線−オイルテンパーからなる伸線工程において、二回目のパテンチング処理の代わりに700℃、60分の焼鈍工程を導入して、最終的に厚さ1.0 mm、幅2.3 mmの断面形状が矩形の線材を準備した。ここで、オイルテンパー処理としては、930℃、45秒の加熱後、60℃のオイル中に焼入する焼入工程と、470℃、60秒の焼戻工程からなる処理を行った。図１に線材の走査電子顕微鏡による顕微鏡組織を示すが、焼戻マルテンサイト中に分散する白色の微細な球状セメンタイトが観察される。また、この組織を拡大し、画像解析により球状セメンタイトの平均粒径と面積率を測定した結果、平均粒径は0.8μm、面積率は2.4％であった。
Examples 1 to 3 (J1 to J3)
From SUP10 steel rolled to 8 mmφ in diameter, consisting of heating (900 ° C)-patenting (600 ° C)-pickling-wire drawing-heating (900 ° C)-patenting (600 ° C)-pickling-wire drawing-oil temper In the wire drawing process, an annealing process at 700 ° C. for 60 minutes was introduced instead of the second patenting treatment, and finally a wire rod having a thickness of 1.0 mm and a width of 2.3 mm and a rectangular cross section was prepared. Here, as the oil temper treatment, a treatment comprising a quenching step of quenching in oil at 60 ° C. and a tempering step of 470 ° C. for 60 seconds after heating at 930 ° C. for 45 seconds was performed. FIG. 1 shows a microscopic structure of a wire material by a scanning electron microscope, and white fine spherical cementite dispersed in tempered martensite is observed. Further, this structure was enlarged, and the average particle diameter and area ratio of spherical cementite were measured by image analysis. As a result, the average particle diameter was 0.8 μm and the area ratio was 2.4%.
実施例４〜５（J4〜J5）
SUP10鋼材を用いて、実施例１〜３と同様の方法で、二回目のパテンチング処理の代わりに、700℃での焼鈍を行い厚さ1.0 mm、幅2.3 mmの矩形の線材を製造した。但し、焼戻マルテンサイトマトリックス中に分散する球状化セメンタイトを調製するため、オイルテンパー処理の焼入前の加熱温度を、実施例４では980℃、実施例5では820℃とした。実施例１と同様に線材の走査電子顕微鏡による顕微鏡組織から画像解析により球状セメンタイトの平均粒径と面積率を測定した結果、実施例４及び５において、平均粒径が0.4μm及び1.2μm、面積率は0.3％及び5.3％であった。
Examples 4 to 5 (J4 to J5)
Using a SUP10 steel material, a rectangular wire material having a thickness of 1.0 mm and a width of 2.3 mm was manufactured by annealing at 700 ° C. in the same manner as in Examples 1 to 3, instead of the second patenting treatment. However, in order to prepare spheroidized cementite dispersed in the tempered martensite matrix, the heating temperature before quenching in the oil temper treatment was 980 ° C. in Example 4 and 820 ° C. in Example 5. As in Example 1, the average particle diameter and area ratio of spherical cementite were measured by image analysis from the microstructure of the wire rod using a scanning electron microscope. As a result, in Examples 4 and 5, the average particle diameters were 0.4 μm and 1.2 μm, and the area The rates were 0.3% and 5.3%.
上記実施例１〜５にかかる厚さ1.0 mm、幅2.3 mmの断面形状が矩形の線材から、呼称径73 mmφの圧力リングを成形し、表２に示す皮膜処理を施した。すなわち、外周面にイオンプレーティングによるCrN皮膜、側面にはリン酸亜鉛系皮膜（実施例２）、リン酸マンガン系皮膜（実施例３）を施した。 A pressure ring with a nominal diameter of 73 mmφ was formed from a wire having a thickness of 1.0 mm and a width of 2.3 mm according to Examples 1 to 5, and a coating treatment shown in Table 2 was performed. That is, a CrN film by ion plating was applied to the outer peripheral surface, and a zinc phosphate-based film (Example 2) and a manganese phosphate-based film (Example 3) were applied to the side surfaces.
比較例１〜５（C1〜C5）
実施例１〜５の伸線工程で、焼鈍工程を導入しない従来のパテンチング処理を２回行う伸線工程で製造した厚さ1.0 mm、幅2.3 mmの断面形状が矩形の線材から成形した圧力リングを比較例１、比較例１のSUP10鋼材の代わりにSi-Cr鋼（JIS SWOSC-V）を使用して比較例１と同様の方法で製造した厚さ1.0 mm、幅2.3 mmの断面形状が矩形の線材から成形し、実施例１〜５と同様に、表２に示す表面処理を施した圧力リングを比較例２〜４、比較例１のSUP10鋼材の代わりに硬鋼線（JIS SWRH62A）を使用して比較例１と同様の方法で製造した厚さ1.0 mm、幅2.3 mmの断面形状が矩形の線材から成形した圧力リングを比較例５とした。比較例１〜５の外周面に全てCrN皮膜を施し、比較例３の側面にリン酸亜鉛系皮膜、比較例４の側面にリン酸マンガン系皮膜を施した。
Comparative Examples 1 to 5 (C1 to C5)
Pressure ring formed from a wire rod having a thickness of 1.0 mm and a width of 2.3 mm formed in a wire drawing process in which the conventional patenting process without introducing an annealing process is performed twice in the wire drawing process of Examples 1 to 5. The cross-sectional shape with a thickness of 1.0 mm and a width of 2.3 mm was manufactured in the same manner as in Comparative Example 1 using Si-Cr steel (JIS SWOSC-V) instead of SUP10 steel in Comparative Example 1 and Comparative Example 1. A pressure ring formed from a rectangular wire and subjected to the surface treatment shown in Table 2 in the same manner as in Examples 1 to 5 is a hard steel wire (JIS SWRH62A) instead of the SUP10 steel in Comparative Examples 2 to 4 and Comparative Example 1. A pressure ring formed from a wire rod having a thickness of 1.0 mm and a width of 2.3 mm and having a rectangular cross-sectional shape manufactured in the same manner as in Comparative Example 1 was used as Comparative Example 5. All the outer peripheral surfaces of Comparative Examples 1 to 5 were coated with a CrN coating, the side surface of Comparative Example 3 was coated with a zinc phosphate coating, and the side of Comparative Example 4 was coated with a manganese phosphate coating.
図２に比較例１の線材の走査電子顕微鏡による顕微鏡組織を示すが、均一な焼戻マルテンサイトが観察されるのみで、実施例１のような微細な球状セメンタイトは観察されなかった。 FIG. 2 shows a microstructure of the wire of Comparative Example 1 by a scanning electron microscope. Only uniform tempered martensite was observed, and fine spherical cementite as in Example 1 was not observed.
熱ヘタリ試験
熱ヘタリ試験は、JIS B 8032-5に基づく。最初に張力を測定し、呼称径にリングを閉じて300℃で3時間加熱した後、再度張力を測定して、その減退率（JISでは接線方向張力減退度）を評価することによって行われる。試験は、実施例１、４及び５並びに比較例１、２及び５について5回行い、その結果の平均値を表２示す。実施例１は平均値でほぼ同じ熱伝導率の比較例１よりも24％、実施例４は4％、実施例５は26％優れた耐熱ヘタリ性を示し、実施例１と５では目標とした4％以下を達成した。なお、バラツキも小さかった。
Thermal sag test The thermal sag test is based on JIS B 8032-5. First, the tension is measured, the ring is closed to the nominal diameter, heated at 300 ° C. for 3 hours, and then the tension is measured again to evaluate the rate of decline (degree of tangential tension decline in JIS). The test was performed 5 times for Examples 1, 4 and 5 and Comparative Examples 1, 2 and 5, and the average value of the results is shown in Table 2. Example 1 shows an average heat resistance of 24% better than Comparative Example 1 with approximately the same thermal conductivity, Example 4 shows 4%, and Example 5 shows 26% better heat resistance. Achieved less than 4%. The variation was small.
熱伝導率測定
熱伝導率は、実施例１、４、５、比較例１、２、５について、レーザーフラッシュ法により測定した。結果を表２に示す。実施例１の熱伝導率はSi-Cr鋼の比較例２よりも高かったが、硬鋼線の比較例５よりは低かった。すなわち、合金元素量に依存することが確認された。
Measurement of thermal conductivity Thermal conductivity was measured for each of Examples 1, 4, 5 and Comparative Examples 1, 2, 5 by the laser flash method. The results are shown in Table 2. The thermal conductivity of Example 1 was higher than Comparative Example 2 of Si—Cr steel, but lower than Comparative Example 5 of hard steel wire. That is, it was confirmed that it depends on the amount of alloying elements.
熱ヘタリ率と熱伝導率の関係を図３に示すが、比較例１、２、５を見る限り、熱伝導率が上がれば熱ヘタリ率も上がる。しかし、実施例１、５は三つの比較例が示すラインよりも下側にあり、同じ熱伝導率でも熱ヘタリ率が低減し、すなわち耐熱ヘタリ性が向上したことが確認できた。 FIG. 3 shows the relationship between the thermal settling rate and the thermal conductivity. As far as Comparative Examples 1, 2, and 5 are seen, the thermal settling rate increases as the thermal conductivity increases. However, Examples 1 and 5 were below the line shown by the three comparative examples, and it was confirmed that the thermal settling rate was reduced even with the same thermal conductivity, that is, the heat settling property was improved.
アルミ凝着試験
アルミ凝着試験は、図４に示す装置（例えば、リケン製トライボリックIV）を用い、リング（圧力リング）を低速で回転する軸上に同軸に載置し、所定の温度に調節したピストン材（AC8A材）を一定の周期で軸方向に往復動させ、リングとピストン材とに面圧荷重を周期的に発生させて、アルミ凝着が発生するまで継続する試験である。アルミ凝着が発生すれば回転軸のトルクが変動し、また温度も上昇する。そのときの負荷サイクル数で寿命を評価する。試験条件としては、試験温度240℃、面圧負荷触れ幅0〜1.1MPa、面圧負荷サイクル数3.3Hz、リング回転速度3.3m/sec（一方向回転）とし、さらに潤滑剤として無添加ベースオイルSAE30をリング表面に0.08cc塗布した。その結果を表２及び図５に示す。耐アルミ凝着寿命は、実施例１の表面処理なし（生材）の場合は、比較例２に比べて51％、実施例２のリン酸亜鉛系皮膜の場合は、比較例３に比べて43％向上した。一方、実施例３のリン酸マンガン系皮膜の場合は、母材の違いによる耐アルミ凝着寿命に差は認められなかった。これはリン酸マンガン系皮膜自体の表面粗さが影響するためと考えられる。
Aluminum adhesion test The aluminum adhesion test is performed by using the apparatus shown in Fig. 4 (for example, Ribbon Tribolic IV) and placing the ring (pressure ring) coaxially on a shaft rotating at a low speed. In this test, the adjusted piston material (AC8A material) is reciprocated in the axial direction at regular intervals, and a surface pressure load is periodically generated between the ring and the piston material until aluminum adhesion occurs. If aluminum adhesion occurs, the torque of the rotating shaft fluctuates and the temperature also rises. The life is evaluated by the number of duty cycles at that time. The test conditions were a test temperature of 240 ° C, a contact pressure load width of 0 to 1.1 MPa, a contact pressure load cycle number of 3.3 Hz, a ring rotation speed of 3.3 m / sec (one-way rotation), and an additive-free base oil SAE30. Was applied to the ring surface by 0.08 cc. The results are shown in Table 2 and FIG. The aluminum anti-adhesion life is 51% in the case of no surface treatment (raw material) in Example 1 compared to Comparative Example 2, and in the case of the zinc phosphate-based film of Example 2 in comparison with Comparative Example 3. 43% improvement. On the other hand, in the case of the manganese phosphate coating of Example 3, no difference was observed in the aluminum adhesion resistance life due to the difference in the base material. This is thought to be due to the influence of the surface roughness of the manganese phosphate coating itself.
1 球状化セメンタイト
2 回転軸
3 リング（圧力リング）
4 ピストン材
5 ヒーター
6 熱電対
7 温度調節器
1 Spheroidized cementite
2 Rotating axis
3 ring (pressure ring)
4 Piston material
5 Heater
6 Thermocouple
7 Temperature controller
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