WO2011148934A1 - 圧力リング及びその製造方法 - Google Patents
圧力リング及びその製造方法 Download PDFInfo
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- WO2011148934A1 WO2011148934A1 PCT/JP2011/061857 JP2011061857W WO2011148934A1 WO 2011148934 A1 WO2011148934 A1 WO 2011148934A1 JP 2011061857 W JP2011061857 W JP 2011061857W WO 2011148934 A1 WO2011148934 A1 WO 2011148934A1
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- pressure ring
- ring
- thermal conductivity
- temperature
- spheroidized cementite
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Classifications
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F02—COMBUSTION ENGINES; HOT-GAS OR COMBUSTION-PRODUCT ENGINE PLANTS
- F02F—CYLINDERS, PISTONS OR CASINGS, FOR COMBUSTION ENGINES; ARRANGEMENTS OF SEALINGS IN COMBUSTION ENGINES
- F02F5/00—Piston rings, e.g. associated with piston crown
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/40—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rings; for bearing races
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16J—PISTONS; CYLINDERS; SEALINGS
- F16J9/00—Piston-rings, e.g. non-metallic piston-rings, seats therefor; Ring sealings of similar construction
- F16J9/26—Piston-rings, e.g. non-metallic piston-rings, seats therefor; Ring sealings of similar construction characterised by the use of particular materials
Definitions
- the present invention relates to a piston ring for an automobile engine, and more particularly to a pressure ring that is exposed to a high heat load environment of a high compression ratio engine and a method for manufacturing the same.
- 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. Since the heat conduction function is closely related to the thermal conductivity of the base material and the surface treatment layer, the ring shape, etc., these can be optimized. Heat resistance and fatigue strength that can maintain the ring characteristics even when exposed to a thermal environment of about °C are also required.
- the piston 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. *
- Japanese Patent Application Laid-Open No. 2009-235561 discloses an appropriate 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 have been proposed that are defined with predetermined parameters.
- the target is a thermal conductivity of 35 W / m ⁇ K or more and a thermal sag (ring tangential tension reduction) of 4% or less, it is difficult to achieve that target.
- automotive parts such as piston rings are required not only for superior characteristics but also for competitive prices. In other words, how to reduce costs is an important issue.
- An object of the present invention is to provide a pressure ring that is excellent in thermal conductivity and heat resistance and can be used in an environment with a high heat load of an engine with a high compression ratio, and that is price competitive. It is another object of the present invention to provide a method for manufacturing the pressure ring.
- Table 1 shows the composition 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.
- the heat resistance is inferior, and it cannot be used as a pressure ring in an environment with a high heat load.
- the cost of steel is generally lower as the amount of alloying elements is smaller.
- 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, basically, a JIS registered material having a small amount of alloying elements is used, and the microstructure is prepared so as to exhibit excellent heat-resistant settling properties even at a high temperature of 300 ° C.
- the present inventor specifically, uses a steel material with a material symbol SUP10 specified in JIS G4801 and anneals the piston ring wire before oil tempering to precipitate spheroidized cementite.
- a steel material with a material symbol SUP10 specified in JIS G4801 and anneals the piston ring wire before oil tempering to precipitate spheroidized cementite.
- the oil tempering conditions it is possible to disperse an appropriate amount of spheroidized cementite in the tempered martensite matrix, to suppress dislocation movement and creep even at 300 ° C., and to improve heat resistance. I came up with it.
- the pressure ring of the present invention is, by mass%, C: 0.45 to 0.55, Si: 0.15 to 0.35, Mn: 0.65 to 0.95, Cr: 0.80 to 1.10, V: 0.15 to 0.25, the balance being iron and inevitable impurities
- a spheroidized cementite having an average particle size of 0.1 to 1.5 ⁇ m is dispersed in a tempered martensite matrix.
- the spheroidized cementite having an average particle size of 0.5 to 1.0 ⁇ m is preferable.
- the dispersion amount of the spheroidized cementite is preferably 1 to 6% by area on the microscopic structure observation surface.
- the thermal conductivity of the pressure ring of the present invention is preferably 35 W / m ⁇ K or more, and the thermal settling rate (degree of tangential tension reduction of the ring) is preferably 4% or less.
- the manufacturing method of the 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, and the balance is iron.
- the annealing step is preferably performed at a temperature of 600 to 720 ° C.
- 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.
- the pressure ring of the present invention achieves both high thermal conductivity and high heat resistance, and even when used in an environment with a high thermal load such as a high compression ratio engine, the piston ring of the piston head is not reduced. Since heat can be efficiently released to the cooled cylinder wall, knocking can be suppressed without adjusting the ignition timing and high heat 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.
- FIG. 2 is a diagram showing a secondary electron image photograph taken by a scanning electron microscope of a cross section of Example 1.
- FIG. 6 is a view showing a secondary electron image photograph of a cross section of Comparative Example 1 by a scanning electron microscope.
- FIG. It is the figure which showed the relationship between the thermal conductivity of Examples 1 and 5 and Comparative Examples 1, 2, and 5 and a thermal settling rate. It is the figure which showed the aluminum adhesion test typically. It is a figure which shows the aluminum adhesion test result of Examples 1-3 and Comparative Examples 2-4. It is a figure which shows the relationship between the composition sum of the alloy element of the steel materials currently used for the piston ring, and thermal conductivity.
- the 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 impurities
- a spheroidized cementite having an average particle size of 0.1 to 1.5 ⁇ m is dispersed in a tempered martensite matrix.
- the above composition is basically a steel material composition of material symbol SUP10 defined in JIS G 4801, and contains a little Cr and V, but has a small total amount of alloy elements, and therefore has a high thermal conductivity. However, the heat resistance is not sufficient.
- 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 in the pressure ring of the ring, excellent heat resistance is achieved, the presence of spheroidized cementite remaining in the matrix after oil temper creates distortion in the crystal lattice, so even at 300 ° C It can be inferred that dislocations are difficult to move.
- the spheroidized cementite has an average particle size of 0.1 ⁇ m or more.
- Residual cementite of about 0.1 ⁇ m or less is not observed as spheroidized cementite having an average particle size of less than 0.1 ⁇ m because it dissolves into austenite in the solution treatment of oil temper treatment.
- the average particle diameter exceeds 1.5 ⁇ m, it is not preferable because it causes fatigue fracture and reduces fatigue strength.
- the average particle size is preferably 0.5 to 1.0 ⁇ m.
- 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 sag ratio (degree of tangential tension reduction based on JIS B 8032-5) is preferably 4% or less.
- the heat conductivity of the commonly used Si-Cr steel is about 31 W / m ⁇ K, and the heat conductivity of about 35 W / m ⁇ K is a conventional flake graphite cast iron that exhibits excellent heat conductivity. Comparable to the thermal conductivity of the piston ring.
- 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.
- JIS B 8032-5 stipulates that the thermal sag rate is 8% or less of the tangential tension decrease under the test conditions of 300 ° C x 3 hours. The target value was about 4%, the same level as Si-Cr steel.
- Steel pressure rings are 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.
- 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.
- the wire used for manufacturing the pressure ring of the present invention is in mass%, C: 0.45 to 0.55, Si: 0.15 to 0.35, Mn: 0.65 to 0.95, Cr: 0.80 to 1.10, V: 0.15 to 0.25, the balance being
- SUP10 steel material
- a wire rod having a predetermined cross-sectional shape is obtained through a series of treatments including annealing and tempering, and is prepared by performing spheroidizing annealing instead of partial patenting treatment.
- 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.
- the annealing process performed instead of the patenting process is preferably performed for 30 to 240 minutes at a temperature of 600 to 720 ° C. below the AC1 point of the Fe—C phase diagram. 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.
- 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 tempering process is a so-called oil quenching-tempering process, 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.
- the quenching process is performed after heating for several tens of seconds to several minutes (eg, 30 seconds to 3 minutes) at a temperature of 820 to 980 ° C.
- the tempering process is performed at a temperature of 400 to 500 ° C. It is preferably performed for about 10 seconds to several minutes (for example, 30 seconds to 3 minutes).
- the particle size and area ratio of spheroidized cementite may fall in a preferable range.
- the pressure ring of the present invention is formed from the above-mentioned wire drawn to a predetermined cross-sectional shape into a free shape of the ring, usually using a cam forming machine, and subjected to heat treatment for removing strain, and grinding the side surface, outer periphery, joint, etc. And processed into a predetermined ring shape.
- surface treatment such as plating or PVD is performed as necessary.
- Examples 1 to 3 Made of SUP10 steel rolled to 8 mm ⁇ diameter, consisting of heating (900 ° C)-patenting (600 ° C)-pickling-wire drawing-heating (900 ° C)-patenting (600 ° C)-pickling-wire drawing-oil temper
- heating 900 ° C)-patenting (600 ° C)-pickling-wire drawing-heating
- 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.
- oil temper treatment a treatment comprising a quenching step of quenching in oil at 60 ° C. and a tempering step of 470 ° C.
- 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 ⁇ m and the area ratio was 2.4%.
- Examples 4 to 5 (E4 to E5) 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. instead of the second patenting treatment in the same manner as in Examples 1 to 3. 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 ⁇ m and 1.2 ⁇ m, and the area The rates were 0.3% and 5.3%.
- a pressure ring with a nominal diameter of 73 mm was formed from a wire rod having a thickness of 1.0 mm and a width of 2.3 mm according to Examples 1 to 5 and having a nominal diameter of 73 mm, and the 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.
- Comparative Examples 1 to 5 (C1 to C5)
- 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 replaced with 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 of 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.
- FIG. 2 shows a microstructure of the wire material of Comparative Example 1 by a scanning electron microscope, and only uniform tempered martensite was observed, and fine spherical cementite as in Example 1 was not observed.
- 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 conducted 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.
- Thermal conductivity was measured for 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 that of Comparative Example 2 of the Si—Cr steel, but was lower than that of Comparative Example 5 of the hard steel wire. That is, it was confirmed that it depends on the amount of alloying elements.
- FIG. 3 shows the relationship between the thermal settling rate and the thermal conductivity. As seen in Comparative Examples 1, 2, and 5, 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.
- 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.
- the adjusted piston material AC8A material
- 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 touch 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.
- a test temperature of 240 ° C a contact pressure load touch width of 0 to 1.1 MPa
- a contact pressure load cycle number 3.3 Hz
- a ring rotation speed 3.3 m / sec (one-way rotation)
- SAE30 additive-free base oil
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Abstract
Description
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。
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。
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。
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。
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。
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。
Claims (6)
- 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ことを特徴とする圧力リング。
- 前記球状化セメンタイトの分散量が、顕微鏡組織観察面において、1~6面積%であることを特徴とする請求項1に記載の圧力リング。
- 熱伝導率が35 W/m・K以上であり、熱ヘタリ率が4%以下であることを特徴とする請求項1又は2に記載の圧力リング。
- 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焼鈍工程を含むことを特徴とする圧力リングの製造方法。
- 前記焼鈍工程が温度600~720℃で行われることを特徴とする請求項4に記載の圧力リングの製造方法。
- 前記オイルテンパー処理工程が焼入温度820~980℃、焼戻温度400~500℃で行われることを特徴とする請求項4又は5に記載の圧力リングの製造方法。
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