WO2004003246A1 - Materiau pour pieces coulissantes auto-lubrifiantes et materiau en fil pour segment de piston - Google Patents

Materiau pour pieces coulissantes auto-lubrifiantes et materiau en fil pour segment de piston Download PDF

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Publication number
WO2004003246A1
WO2004003246A1 PCT/JP2003/008309 JP0308309W WO2004003246A1 WO 2004003246 A1 WO2004003246 A1 WO 2004003246A1 JP 0308309 W JP0308309 W JP 0308309W WO 2004003246 A1 WO2004003246 A1 WO 2004003246A1
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graphite
mass
self
observed
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PCT/JP2003/008309
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English (en)
Japanese (ja)
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Etsuo Fujita
Kunichika Kubota
Yoshiki Masugata
Yoshihiro Minagi
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Hitachi Metals, Ltd.
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Priority to KR1020047021503A priority Critical patent/KR100701812B1/ko
Priority to DE60325602T priority patent/DE60325602D1/de
Priority to JP2004517335A priority patent/JP4273462B2/ja
Priority to AU2003244199A priority patent/AU2003244199A1/en
Priority to EP03761840A priority patent/EP1529852B1/fr
Priority to US10/519,981 priority patent/US20060048865A1/en
Publication of WO2004003246A1 publication Critical patent/WO2004003246A1/fr

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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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • 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
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

Definitions

  • the present invention relates to sliding parts such as piston rings, cylinder liners, and vanes mounted on internal combustion engines such as ordinary plain bearings, roller bearings, ball bearings, gears, dies, and automobile engines. Belongs to the material used. Background art
  • sliding parts such as cylinder liners and vanes are provided with materials having excellent wear resistance.
  • the piston rings used in internal combustion engines, especially in automobile engines are shifting from conventional iron-made to so-called steel piston rings, which are used by processing steel wires into rings.
  • a wire obtained by subjecting an ingot having a predetermined composition to hot working such as forging and hot rolling is further drawn into a steel wire material corresponding to the small cross-sectional shape of the piston ring, and the hardness is adjusted.
  • Biston rings are generally manufactured by bending into a ring with a fixed curvature.
  • top ring, the second ring, and the oil ring are attached to one piston from the combustion chamber side, but in Japan, the top ring and the oil ring, which are severe parts, are The high functionality of Steeli-Dani is permeating.
  • post-internal combustion engines such as electric vehicles
  • diesel engines with higher internal cylinder pressures have lower environmental impact than gasoline-powered vehicles if gas oil quality is improved and exhaust gas filters are upgraded, so the sliding performance can be used for more severe diesel engines. May be called for improvement.
  • a further reason for the shift to steel is to reduce the frictional force loss by reducing the thickness of the ring structure to improve the environmental performance of the engine, and consequently the need to increase the mechanical strength. Behind them, or improved wear resistance.
  • environmental regulations for Cr plating which is the mainstream for iron, are becoming stricter, resulting in less harmful effects and nitriding.
  • steelification is accelerating due to the necessity of conducting steelmaking.
  • Non-Patent Document 1 Hideki Saito and 2 others, “Study on Diesel Engine Wear Under Severe Operating Conditions", Japan Society of Mechanical Engineers, Kyushu Branch, 2001 Research Presentation Lecture (1 99 9 9) (Internet ⁇ URL:
  • Patent Document 1 Japanese Patent Application Laid-Open No. H10-0-030726
  • Patent Document 2 Japanese Patent Publication No. 5-8-0 4 6 5 4 2
  • Patent Document 2 mainly propose a composition design that increases the amount of Cr-based carbides in steel, which is excellent in terms of performance and cost, by adding Cr of 10% or more mainly. Suggest an area.
  • the wear resistance is dramatically improved by increasing the amount of carbide, there is concern that the effect of improving seizure resistance is insignificant and that the machinability is degraded and the productivity is adversely affected. You. Therefore, it is necessary to perform surface treatment such as PVD However, a rise in cost is inevitable.
  • the present invention provides a sliding component material that has improved seizure resistance and also has excellent wear resistance by using a nitriding treatment, and is applied to a biston ring thereof.
  • An object of the present invention is to provide a wire rod for a piston ring that has excellent sulfuric acid corrosion resistance and manufacturability in addition to dynamic characteristics and has a low coefficient of friction.
  • the present inventors have described in detail the sliding behavior of various applied sliding components, particularly sliding components exposed to a sliding environment under fluid lubrication such as a piston ring. We investigated and examined. As a result, we found the optimal morphology for improving seizure resistance and lowering the coefficient of friction, and by finding out the composition that is effective in achieving that structure while taking into account the sulfuric acid corrosion resistance. Invented the invention.
  • C 0.4% or more and less than 1.5%
  • Si 0.1 to 3.0%
  • Mn 0.3 to 3.0. %
  • Cr 0 to 0.5%
  • Ni 0.05 to 3.0%
  • A1 0.3 to 2.0%
  • One type consists of steel containing 0.3 to 20% in total amount (Mo + W + V) and Cu: 0.05 to 3.0%.
  • the average particle size of graphite observed in the microstructure section is 3 am
  • a sliding component material having the following self-lubricating properties is provided.
  • the area ratio of graphite observed in the tissue section is 1% or more, and the average particle size is 3 ⁇ or less. Further, it is preferable that no V-carbide is observed in the tissue section.
  • At least one selected from the group consisting of Mo and W is 0.3 to 5.0% in total, and V: less than 0.1%.
  • the preferred amount of A1 is 0.7 to 2.0%.
  • the steel contains Mo: 1.5 to 3.0% and Co: 10% or less. Is preferred.
  • the sulfur (S) and Ca content of the steel are preferably S: 0.3% or less, and Ca: 0.01% or less. It is preferable to use as.
  • C 0.4% or more and less than 1.5%
  • S i 0.:!-3.0%
  • M n 0.1-3. 0%
  • Cr 0 to 0.5%
  • Ni 0.05 to 3.0%
  • A1 0.3 to 2.0%, selected from the group consisting of Mo, W and V Contains at least one of 0.3 to 20% in total amount (Mo + W + V), Cu: 0.05 to 3.0%, and the average particle size of graphite observed on the tissue surface is 3 ⁇ m
  • a wire for a piston ring made of the following steel is provided.
  • the distribution state of the sulfide inclusions observed in the cross section of the structure parallel to the outer peripheral surface is determined by the parallelism between the straight lines passing over the maximum diameter of each sulfide inclusion.
  • the area ratio of graphite occupied in the cross section of the structure of the wire for a piston ring is 1% or more, and the average particle size is 3 ⁇ or less.
  • the wire for a piston ring preferably contains Co: 10% or less, or further contains S: 0.3% or less, and Ca: 0.01% or less, and may be used after being subjected to nitriding treatment. preferable.
  • An important feature of the present invention is that, for sliding parts typified by piston rings, a steel structure in which fine and moderate graphite is precipitated has been realized as an optimal means for improving seizure resistance and reducing the friction coefficient. That is. In other words, it is intended to improve the durability performance by taking into account the peculiarity of the friction behavior between the piston ring and the cylinder, in order to compensate for it, and to improve the non-surface treatment material or surface treatment cost. Thus, even with the advantageous nitriding material, sufficient effects can be achieved with respect to the reduction in seizure resistance and friction coefficient, which were insufficient with conventional technologies.
  • the mainstream of sliding parts is a fluid lubrication design in which a fluid film of oil, water, etc. is constantly formed between the usually severely rubbing mechanical elements.
  • This fluid film formation utilizes the buoyancy of a fluid that moves relative to each other like an airplane. If the viscosity and relative speed of the fluid increase, the fluid film interposed between the sliding parts becomes thicker. This protects the mechanical elements from friction.
  • the pressure distribution generated on the surface of the plate opposing the substrate has a boundary condition where the pressure is 0 at the edge of the plate, and in order to maintain lubrication, that is, to generate a positive pressure distribution,
  • the pressure distribution must be a convex function and can be described by the following conditions.
  • Equation (3) has three terms.
  • the first and second terms include the relative velocity u, and correspond to the wedge action and the expansion / contraction action described above.
  • the third term that does not include u is the term indicating the squeeze action, which has the possibility of functioning even if the relative speed between the Biston ring Z cylinders becomes zero.
  • the present inventors have found that the effect can be further enhanced by forming a large number of hole-shaped structures on the sliding surface thereof.
  • a large number of fine holes are provided on the sliding surface, even if the relative velocity is zero and the fluid film is broken, the fluid in the holes will instantaneously elapse over the next time. It is squeezed out on the dead surface of the fluid, and a squeezing action can be obtained by a large decrease in the film thickness of the moved fluid.
  • seizure in the vicinity of the vertical dead center of the reciprocating motion can be suppressed, and the friction coefficient can be reduced.
  • the graphite precipitate structure of the present invention has been determined by paying attention to this action and effect. That is, the graphite structure of the present invention first acts as a lubricating phase having a solid lubricating action, but at the same time, it is also important that the graphite film retains an oil film as pores when the graphite falls off. This is the above-mentioned squeezing action for improving the performance. As described above, the oil film is formed stably with respect to pressure fluctuations, and the effect is enhanced by arranging holes on the surface of the sliding surface.
  • the graphite precipitate structure of the present invention is also effective in preventing adhesion wear with an aluminum piston, which has recently become a problem when applied to the piston ring. In other words, since aluminum has almost no solid solubility limit in carbon, the adhesion reaction is suppressed.
  • the sliding component material of the present invention disperses graphite on the surface of the structure.
  • F It is important that the observed average particle size of graphite is 3 // m or less. This is because if the average particle size exceeds 3 im, the periphery of the graphite will be damaged during the sliding, and there is a concern that the fragments may enter the sliding surface.
  • the area ratio of graphite observed on the tissue surface is 1% or more. More preferably, for relatively coarse graphite having a particle size of 1 ⁇ m or more, the average particle size is 5 or less, or the area ratio is less than 5%.
  • the lubrication effect due to the formation of holes causes the fluid film to decrease due to the above-mentioned effects, and any of them loses the effect.
  • the means of the present invention is effective especially in reciprocating motion where it is difficult to form a continuous fluid lubricating film, such as with an internal combustion engine.
  • Graphite deposition is effective in an environment where transient frictional behavior occurs, such as between a piston ring and a cylinder, where the area near the point is a temporary state and immediately shifts to an environment rich in lubricating oil. I do.
  • Graphite steel itself has been reported for a long time, and these are mainly alloys to which Si and Ni have been added.However, there are a number of graphite precipitation treatments that maintain a temperature of 600 ° C or more. It took more than 10 hours.
  • the present invention is characterized in that cementite is easily decomposed in order to complete precipitation of black tin at the level of several hours, and an appropriate amount of A1 is added to Ni.
  • A1 has a high diffusion rate in iron, and the addition of A1 increases the diffusion rate of vacancies and shortens the time required to form aggregates of vacancies where graphite is deposited. .
  • the present invention has made it possible to precipitate graphite in a short time. It is also easy to deposit graphite only on the surface by carburizing or the like.
  • A1 is also an element having nitriding hardening ability, which is advantageous in designing an alloy of nitrided hardened copper.
  • Cr is also an element used as a nitriding hardening element. Since Cr not only inhibits graphite formation, which is the core technology of the present invention, but also significantly reduces sulfuric acid corrosion resistance. Avoid using as much as possible. Therefore, A1 used in the present invention is an important contained element.
  • the nitride layer has a defect such as graphite with a particle size of 10 m or more, such as the case of applying a nitriding treatment to graphite steel, the nitriding layer becomes brittle. Therefore, there were difficulties in depositing graphite on nitrided steel. Therefore, in the present invention, efforts were made to refine the precipitated graphite in order to realize the nitrided steel. For the miniaturization of the precipitation graphite, and (1) refining by processing strain, (2) the addition of A 1 2 ⁇ 3 like inclusions, (3) BN, deposited nuclei T i C, etc., three methods Are listed.
  • JP-A-11-246940 discloses a method of dispersing TiC.
  • Takashi Iwamoto et al. In “Iron and Steel Vo 1.84 (1998) p. 57” show graphite precipitation using BN as a nucleus.
  • the second phase precipitates at a high temperature with a high diffusion rate of 1000 ° C or more, so it is difficult to maintain the fine uniformity of graphite, and it is difficult to use high alloys with severe component segregation. Difficult to apply.
  • the present inventors have conducted various studies to achieve the miniaturization of graphite, and as a result, have found that the Cu—A 1 metal precipitate phase in the structure works effectively.
  • This is a phenomenon in which the second phase acts as the nucleus of precipitated graphite, as described above.Since this Cu-A1 phase precipitates at a low temperature of 800 ° C or less, a fine graphite structure can be formed stably and quickly. .
  • the present invention specifically, by adding Cu and A1 at a level at which the brittle phenomenon does not occur, it is possible to form a graphite structure with less strength deterioration and acting as a lubricating phase.
  • Cu also contributes to the improvement of sulfuric acid corrosion resistance.
  • C is an important element that forms a solid solution in the matrix to impart strength, partially forms carbide, and the rest forms graphite to increase wear resistance and seizure resistance. For this there is little At least 0.4% is required. However, if the temperature exceeds 1.5%, the melting point decreases, making it difficult to homogenize the structure by diffusion annealing to eliminate solidification segregation, such as heating the ingot at around 1200 ° C for several tens of hours. Become. Therefore, C is set to 0.4% or more and less than 1.5%. Preferably, it is 0.5% or more and less than 1.3%.
  • Si is usually added as a deoxidizing agent, it is added here as an element for accelerating graphite precipitation and has an effect of improving the sulfuric acid corrosion resistance. Therefore, the lower limit is set to 0.1%. On the other hand, it also affects the tempering softening behavior of the steel, and the effect of Si is particularly important for low alloy steels.
  • the preferable Si content for preventing temper softening and increasing the heat resistance is 1.0% or more. However, the point will rise if it is added excessively, so the upper limit of Si is set to 3.0%. Therefore, S U 0.
  • it is 0.5 to 3.0%, more preferably 1.0 to 3.0%.
  • Mn like Si, is used as a deoxidizing agent, and at least 1% is required. However, excessive addition impairs graphite precipitation. Therefore, the upper limit was set at 3.0%. Therefore, Mn is set to 0.1 to 3.0%.
  • Cr is an effective nitridation hardening element, it is an element that suppresses the decomposition of metastable cementite, not only strongly inhibits the precipitation of graphite, but also significantly reduces sulfuric acid corrosion resistance. Need to be regulated. Therefore, in the present invention, it is 0 to 0.5%, preferably 0 to 0.3%.
  • Ni is an element that promotes the formation of graphite and is also a useful element in suppressing red hot embrittlement that occurs in the Cu-added steel, but on the other hand, in order to increase the solid solubility limit of C in Fe, the annealing state Is an element that inhibits workability in Therefore, it was set to 0.05 to 3.0%. Preferably, it is 0.6-1.5%.
  • a 1 is a graphite-forming element, which aids in the diffusion of vacancies, and also serves as a Cu-A1 phase together with Cu to form graphite nuclei, causing rapid and fine precipitation. Since it is an effective element, it is necessary to add 0.3% or more.
  • a 1 is specified to be 2.0% or less in order to raise the point similarly to S i. Therefore, in the present invention, the addition range is limited to 0.3 to 2.0%. Preferably, 0.7 to 2. 0%.
  • Mo is a carbide forming element that does not inhibit graphite as compared with Cr, and is an element that imparts heat resistance.
  • Carbides serve to enhance dimensional stability, for example, by constraining the matrix during thermoforming performed after bending in the piston ring manufacturing process. However, excessive amount of Mo-added rice cake suppresses the decomposition of cementite like Cr.
  • Mo has little effect of the above-mentioned inhibition, and on the other hand contributes significantly to the improvement of heat resistance and contributes to dimensional stability during heat treatment.
  • the upper limit is set to 20% to prevent graphite precipitation.
  • V and W have the same effect as that of Mo, in the present invention, at least one selected from the group consisting of Mo, W and V is 0.3 to 20% in total amount. It can be.
  • the composite (Mo + W) of Mo and W or the single addition (Mo + W) is 0.3 to 5.0%, and V is less than 0.1%.
  • Mo promotes the squeezing action of graphite and helps to form a fluid film under high pressure, thereby improving seizure resistance and reducing the coefficient of dynamic friction.
  • the amount of Mo alone added is 1.5 to 3.0%.
  • Cu is an important element for the present invention together with A1, because Cu is effective in precipitating the metal phase of Cu—A1 and stably and rapidly forming a fine lead structure. It also has the effect of improving sulfuric acid corrosion resistance. Therefore, it is necessary to reciprocally adjust the content also serving as the amount of A1, and to obtain the effect, it is necessary to add 0.05% or more, and preferably 0.2% or more. On the other hand, if Cu is added excessively, the hardness at the time of annealing will increase, and workability will be impaired. Therefore, in the present invention, the composition range is 0.05 to 3.0%, and preferably 0.2 to 3.0%.
  • sulfur (S) is known as a technology for organizing and adding as an extreme pressure additive in engine oil to prevent seizure.
  • the present inventors have found that the presence of MnS and red sulfide (sulfide) in the steel allows the sulfur (S) to form an in situ sulfide on the new surface created on the friction surface by frictional heating. They formed a film and found that this was effective in improving lubrication performance. According to this means, since the lubricating substance is scattered inside the material, it is not necessary to add a large amount of the lubricating substance to improve the lubricating performance at a necessary local portion. It can be expected to function semi-permanently because the effect does not disappear.
  • the conventional means for increasing the amount of Cr-based carbide in steel for piston rings is, in other words, the contact area with the cylinder liner is small, and the sliding energy per unit area is high.
  • the aim is to increase the performance and balance with the cylinder liner. This improves the seizure resistance, but essentially increases the contact area by promoting wear on the cylinder liner side due to non-uniform contact, resulting in abnormal local surface pressure.
  • the aim is to avoid rising.
  • it is a technology that improves the familiarity of the piston ring at the beginning of installation, and has few functions as wear characteristics that require durability such as adhesive wear.
  • seizure resistance can be further improved by adding an appropriate amount of sulfur (S).
  • sulfur (S) is mostly combined with Mn to form MnS, which acts on lubricants such as engine oil to exert a lubricating effect, lowering the coefficient of friction and improving seizure resistance .
  • seizure is a phenomenon in which the frictional surface temperature rises due to frictional heat and the atoms move between the materials due to thermal vibrations, causing sticking.
  • the content of sulfur (S) is effective, but if added excessively, the mechanical properties deteriorate, and for example, there is a concern that the wire may break during the drawing process of steel wires for steel biston rings.
  • the upper limit is preferably 0.3%.
  • the content is desirably 0.01 to 0.3%, and more desirably 0.03 to 0.3%.
  • the present inventors have found that in order to obtain a material obtained by adding sulfur (S) to 0.3%, it is necessary to increase the forging ratio applied to the manufacturing process from the viewpoint of mechanical properties. I also found something desirable. In other words, it is effective for improving the mechanical properties of sliding parts, and in particular, for steel biston rings obtained by bending steel wires, it suppresses breakage and breakage in the bending process. It is also an effective means of doing so.
  • the forging ratio is defined as a reduction in area from an ingot to a piston ring product in the piston ring manufacturing process.
  • (ingot cross-sectional area before forging) / (product cut after bending) Area) compared to the cross section perpendicular to the direction in which the steel is forged and stretched, that is, the small cross section in the final biston ring product.
  • the reduction in area from steel wire to piston ring products due to bending is negligible for achieving the effects of the present invention, and is calculated by (ingot cross-sectional area before forging) / (before bending (forging * elongation). (After) steel wire cross-section). The higher the number of these forging ratios, the more the forging is progressing.
  • a sulfide such as Mn S in the starting structure, a large number of spherical or spindle-shaped sulfides are present at the grain boundary triple point of the solidified cell structure, and the orientation is random.
  • the orientation of the sulfide changes, and the mechanical properties are improved.
  • Increasing the forging ratio increases the orientation of the sulfide in the length direction of the steel wire.
  • the sulfide expands along the circumferential stress that mainly acts on the piston ring, resulting in mechanical properties. Is hardly deteriorated.
  • This effect is particularly remarkable for stretched sulfides, that is, salifides having an aspect ratio (maximum diameter / minimum diameter) of 3 or more.
  • the circumference of a sulfide having an aspect ratio of 3 or more Poor orientation in the direction leads to deterioration of mechanical properties.
  • the sulphide observed on the tissue surface parallel to the outer peripheral surface of the biston ring is determined by the degree of parallelism (the angle on the acute angle side) between the straight lines passing over the maximum diameter of each sulfide-based inclusion.
  • the temperature is set to within 30 degrees, a material for sliding parts that is particularly effective as a wire for a piston ring can be obtained. For example, it is preferable to achieve a forging ratio of 500 or more.
  • Figure 5 shows a sketch of the microstructure of a forged steel with a forging ratio of 1 (as-forged) and 500 forged at a magnification of 400 times without corrosion, and a view of the sulfide-based inclusions at that time.
  • the schematic diagram which performed the parallelism measurement is shown.
  • Aspect ratio Two optional sulfide-based inclusions of 3 or more are selected, and the straight line (A, B line) passing through the maximum diameter of each is measured, and the acute angle formed by each other is measured. Then measure it. This measurement is performed over at least 10 fields of view, and the maximum value of the angle is defined as parallelism.
  • the A 'line parallel to the A line may be measured as an auxiliary line.
  • the definition that one sulfide-based inclusion is regarded as one is defined as one that is considered to be connected by observation with a 400 ⁇ optical microscope, and a straight line passing through the maximum diameter is used as a measurement line.
  • Fig. 5 it can be seen that the sulphide inclusions with a forging ratio of 1 exceeding 30 degrees are present, but those with a forging ratio of 500 are all less than 30 degrees.
  • the number 30 degrees is a number designed for fracture mechanics.
  • Fig. 6 feG.i.Irwm (Analysis of Stresses and Strains Near the End of a Crack Transversing a Plate, Trans.ASME, Ser.E, J. Appl.Mech., Vol. 24, No. 3 (1957), pp. This figure shows how the stress intensity factor changes when an angle occurs in the stress direction and in the crack propagation direction, calculated analytically by It is.
  • inclusions can be regarded as cracks due to poor mechanical bonding, it is clear that it is important to control the variation in the orientation of the inclusion distribution to 30 degrees or less. Then, it is understood that it is important to make the orientation of the elongated inclusions uniform.
  • the content is preferably 0.0001% to 0.01%, more preferably 0.0005% to 0.01%.
  • the addition of S and Ca is effective in improving machinability and grindability in addition to seizure resistance.
  • the dispersion of MnS and the precipitation of graphite improve the machinability of steel, it is easy to form corners with a small radius of curvature, which are difficult to form by grinding. This makes it easier to manufacture an improved biston ring.
  • the sliding component material and the piston ring wire of the present invention can also contain Co for the effect of enhancing corrosion resistance, particularly sulfuric acid corrosion resistance. Further, like Mo, it promotes the squeezing action of graphite and helps to form a fluid film under high pressure, which has the effect of increasing seizure resistance and lowering the coefficient of dynamic friction.
  • the content is preferably 0.5% or more.
  • the content is preferably set to 10% or less. desirable. More preferably, it is 2 to 5%.
  • the steel constituting the material for sliding parts and the wire rod for biston rings of the present invention is, for example, a steel that satisfies the content of each of the above-described element types, and that the remainder is substantially Fe.
  • the total amount should be 10% or less, and more preferably 5% or less.
  • steel with the remaining Fe and unavoidable impurities can be applied.
  • the area ratio of nonmetallic inclusions in the texture plane is set to 2.0% or less, it is possible to prevent breakage in a drawing step of processing into a steel wire rod and to reduce the wire rod. It is effective in preventing breakage when forming into a coil shape. In particular, it is effective for the production of piston rods that involve the production and processing of fine wire rods, and is desirable as a range that enables production with a high operating rate.
  • the nitriding treatment is effective in further improving seizure resistance and abrasion resistance as an effect added to the present invention, but in the case of the present invention, excellent seizure resistance is achieved regardless of the presence or absence of the surface treatment.
  • other surface treatments such as PVD and Cr plating may be combined.
  • these surface treatments are conventionally applied to the contact surface between the piston ring and the cylinder liner, which is the main sliding surface, but not to the friction surface with the piston.
  • adhesion wear cannot be prevented.
  • the material of the present invention is used, sufficient seizure resistance is exhibited even without surface treatment, and the adhesion reaction is suppressed, so that the material is particularly effective for a piston ring.
  • the graphite phase exists in the material of the present invention, it is immersed in, for example, a CuCl 2 solution.
  • a so-called intercalation treatment in which another molecule or ion is inserted between the molecular layers of the layered molecular structure of the black sharp can be performed, and the sliding characteristics can be further improved.
  • the graphite after the intercalation treatment also serves as a polymer polymerization catalyst, lubrication treatment with a polymer coat (polymer coating treatment) can be performed, or only the intercalation treatment is performed in advance to polymerize the lubricating oil.
  • FIG. 1 is a photograph of a structure of a microphone opening showing a distribution state of graphite observed in a section of a structure of a material of the present invention (sample No. 3).
  • Fig. 2 is a photograph of the microstructure of the microphone opening showing the distribution of graphite observed in the microstructure section (different field of view) of the same material as that shown in Fig. 1.
  • FIG. 3 is a microstructure photograph showing the distribution state of graphite observed in the cross section of the structure of the comparative example material (sample No. 14).
  • Fig. 4 is a photograph of the microstructure of the microphone opening showing the distribution of graphite observed in the cross section of the same material as the material shown in Fig. 3 (another field of view).
  • FIG. 5 is a sketch diagram and a schematic diagram of a microstructure photograph illustrating the parallelism of the sulfide-based inclusions.
  • FIG. 6 is a diagram for explaining the effect of the angle between the stress direction and the crack propagation direction on the stress intensity factor.
  • FIG. 7 is a schematic diagram illustrating an ultra-high pressure friction and wear test method.
  • FIG. 8 is a schematic diagram illustrating a reciprocating wear test method.
  • FIG. 9 is a Stribeck diagram showing the relationship between the reciprocal of the load and the dynamic friction coefficient, and is a diagram illustrating a lubricated state.
  • Samples No .:! To 6 are examples satisfying the present invention, and samples No. 11 to 16 are comparative examples.
  • Sample No. 16 is a material equivalent to JIS-SUS 440 B, and is a currently used piston ring material.
  • sample No. 13 could be manufactured, but test pieces could not be manufactured because the steel material was destroyed in the subsequent hot working process.
  • FIG. 1 to 4 are micrographs showing the distribution of graphite in samples No. 3 and No. 14.
  • FIG. Fine graphite is precipitated in the matrix structure of sample No. 3, but the graphite of sample No. 14 is coarse. This is because when an appropriate amount of Cu and A1 is included, a fine Cu-A1 phase is precipitated prior to graphite precipitation, and graphite is precipitated using the nucleus as a nucleus, resulting in a fine graphite distribution. If Cu or A1 is insufficient, this mechanism does not work, and graphite precipitates coarsely.
  • Table 2 shows the distribution of graphite, including other samples. No graphite was observed in the structures of Sample Nos. 11, 12, 15, and 16.
  • Friction speed 2m / sec
  • Friction surface pressure initial pressure 1.5MPa, 0.5MPa every minute
  • Abrasion resistance was evaluated by a backward wear test. This method measures the wear width at the time by rubbing a separately prepared test piece of 8 mm in diameter and 20 mm in length with a counterpart material (FC250) of 2 Omm in diameter by reciprocating motion.
  • Figure 8 shows the other test conditions.
  • reference numeral 1 denotes a sample
  • 2 denotes a partner material
  • F denotes a load
  • OIL denotes a lubricating oil.
  • Lubricating oil (supplied by dripping); motor oil # 30
  • Table 2 shows the measurement results of the scuff load, kinetic friction coefficient and wear width together with the nitriding hardness.
  • Sample Nos .: to 6 satisfying the present invention have excellent scuff resistance and abrasion resistance because of high scuff load and narrow wear width.
  • Samples Nos. 3 to 6 also have low values of the dynamic friction coefficient, and exhibit extremely excellent characteristics as sliding members.
  • all the comparative samples which do not satisfy the graphite distribution of the present invention have poor seizure resistance.
  • the lack of wear resistance of Samples Nos. 11 and 15 is due to the low content of both Cr and A1, which are elements having nitriding hardening ability, and low nitriding hardness. It is.
  • Example 1 the sample prepared in Example 1 was subjected to a seizure test under the same conditions without performing the nitriding treatment.
  • Table 3 shows the results.
  • the seizure resistance of Sample Nos. 1 to 6 satisfying the graphite distribution of the present invention is exhibited regardless of the presence or absence of the surface treatment, even if graphite is present, the scuff load of the coarse Comparative Sample No. 14 is low.
  • Observation of the rubbing surface of this sample No. 14 after the test revealed that the periphery of the graphite had been damaged, and it was probable that the shards entered the friction surface and had poor sliding characteristics.
  • Sample No. 1 and Sample No. 15 in the composition shown in Table 1 were formed into coils with a diameter of 5.5 mm by hot rolling, and then drawn and cold-rolled to form a 1.5 mm X 3.1 mm flat wire. Finished in shape. Sample No. 1 could be processed without any problem, but Sample No. 15 had poor cold workability and broke during the drawing process. Image analysis of the area ratio of non-metallic inclusions occupying in both yarn and fabric surfaces in the state of the billet before drawing was performed on the structure plane perpendicular to the next drawing and rolling direction. 1 is 1.86%, sample No. 15 was 2.23%, and the cause of the fracture was that in addition to its high sulfur (S) content, the area ratio of nonmetallic inclusions exceeded 2.0%.
  • S high sulfur
  • Samples Nos. 1 to 6, 11, and 12 in Table 1 were finished in the process shown in Example 2 into a 1.5 mm X 3.1 mm flat wire shape, and quenched at 1 000 ° C for 30 minutes. And tempering were performed to a hardness of about 510HV. Thereafter, cutting was performed 10 times with a grinding wheel cutter at a rotation speed of 10,000 rpm and a feed speed of 1 mmZ seconds, and the occurrence of burrs was investigated. Table 4 shows the frequency of occurrence.
  • a material with a high forging ratio and a parallelism of sulfide-based inclusions of 30 degrees or less has excellent mechanical properties and is effective in suppressing rupture, which is a concern during bending from a wire to a ring shape. Then, when these wires having excellent bending workability are bent and formed into a piston ring shape, the parallelism of the sulfide-based inclusions observed on the tissue surface parallel to the outer peripheral surface is obtained. In the case of the wire rod, there was no substantial change in the wire ratio.
  • the degree of parallelism of the sulfide inclusions observed in these wire states is also reflected in the piston ring state after bending.
  • the form of sulfide-based inclusions with a parallelism of 30 degrees or less depends on the mechanical properties. It is effective for improvement, and is particularly preferable for wires for biston rings.
  • these ingots were subjected to hot working to obtain a linear material having a cross-sectional dimension of 9 mm X 9 mm (forging ratio: about 598).
  • a predetermined quenching and tempering treatment was performed after the annealing treatment to adjust the hardness to about 40 HRC.
  • the microstructure surface of the quenched and tempered linear material was observed without corrosion, and the distribution state of graphite (average particle size, area ratio to the structure) was examined.
  • the distribution situation was investigated by using image analysis from an image of 100 visual fields observed with a 100 ⁇ optical microscope.
  • the graphite precipitation of all samples No. 21-23 was fine.
  • Table 7 shows the distribution of graphite.
  • the average particle size was 1 ⁇ m or less and the area ratio was 1 to 4%.
  • the relatively coarse graphite having a particle size of 1 IX m or more has an average particle diameter of 1 to 1.5 / im and an area ratio of less than 1% in all samples. In each sample, the ratio of the area of relatively coarse graphite of 1 m or more to the total area of graphite was less than 1/4, indicating that fine graphite occupies most of the precipitated graphite. .
  • FC 250 JIS mouse rat iron
  • Fig. 9 is a curve called the Stribeck diagram, in which the "load characteristic" indicating the condition of the load applied to the friction sliding portion is plotted on the horizontal axis, and the friction coefficient is plotted on the vertical axis. This makes it possible to know the lubrication state.
  • the horizontal axis can be represented by the reciprocal of the load.
  • the right side of the plot (extreme value) with the lowest coefficient of friction (low load side: the range indicated by the arrow) is the area where the lubricating film is not destroyed and fluid lubrication occurs.
  • the left side is the area where the fluid film is broken and the solid lubrication is mixed with the fluid lubrication due to the contact between the solids. Therefore, the lower the plot (extreme value) of the coefficient of friction shifts to the left side of the graph, the higher the load, the more the fluid film is not broken, indicating that fluid lubrication is possible. From the results in FIG. 9, it is found that the sample No. 22 having a higher Mo content than the sample No. 21 retains the fluid film even on the higher load side. In addition, it can be seen that in the sample No. 23 having a high Co content, the fluid film is retained even on the higher load side. This indicates that Mo and Co have the effect of promoting the squeezing action described above.
  • the leftmost plot of each curve corresponds to the load at which the test was stopped due to seizure.
  • Sample Nos. 22 and 23 the above plots shifted to the left (high load side) due to the addition of Mo and Co, and the seizure resistance was further improved.
  • the kinetic friction coefficient is also low overall, and the addition of Mo and Co further improves good sliding characteristics due to graphite precipitation.
  • self-lubrication imparts excellent seizure resistance even without surface treatment, has a low friction coefficient, and reduces energy loss due to friction, so that it can be applied to various sliding parts.
  • By adjusting the morphology of the sulfide inclusions it is particularly effective as a piston ring, reducing the aggression of cylinder liners and pistons, and improving the environmental performance and durability of the internal combustion engine. Big against Play a contribution.
  • it has excellent workability such as machinability in the manufacturing process, and can reduce manufacturing cost and lead time, making it a material for sliding parts that is excellent in both performance and manufacturing, and is a very useful technology in industry. .
  • the material of the present invention is used for sliding parts such as a piston ring, a cylinder liner, and a vane mounted on an internal combustion engine such as a plain bearing, a roller bearing, a ball bearing, a gear, a mold, and an automobile engine.
  • an internal combustion engine such as a plain bearing, a roller bearing, a ball bearing, a gear, a mold, and an automobile engine.

Abstract

L'invention concerne un matériau pour pièces coulissantes comprenant un acier qui renferme, en pourcentage de masse, 0,4 % ou plus et moins de 1,5 % de C, de 0,1 à 3,0 % de Si, de 0,1 à 3,0 % de Mn, de 0 à 0,5 % de Cr, de 0,05 à 3 % de Ni, de 0,3 à 2,0 % d'Al, de 0,3 à 20 % constitués par la somme (Mo + W + V) d'un ou de plusieurs des éléments du groupe composé de Mo, W et V, et de 0,05 à 3,0 % de Cu, et des particules de graphite observées dans la face structurelle de ce matériau dont le diamètre moyen est de 3 νm ou moins. La région des particules de graphite observées dans la face structurelle représente de préférence 1 % ou plus de la région de la face structurelle, les particules de graphite ayant un diamètre moyen de 3 νm ou moins. L'acier peut en outre contenir 0,3 % ou moins de S et 0,01 % ou moins de Ca, et est de préférence soumis à un traitement de nitruration avant emploi. Ce matériau pour pièces coulissantes est utilisé sous forme de fil pour des segments de piston.
PCT/JP2003/008309 2002-07-01 2003-06-30 Materiau pour pieces coulissantes auto-lubrifiantes et materiau en fil pour segment de piston WO2004003246A1 (fr)

Priority Applications (6)

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KR1020047021503A KR100701812B1 (ko) 2002-07-01 2003-06-30 자기 윤활성을 갖는 슬라이딩 부품용 재료 및 피스톤 링용선재
DE60325602T DE60325602D1 (de) 2002-07-01 2003-06-30 Material für gleitbauteile mit selbstschmierung und drahtmaterial für kolbenring
JP2004517335A JP4273462B2 (ja) 2002-07-01 2003-06-30 自己潤滑性を有する摺動部品用材料およびピストンリング用線材
AU2003244199A AU2003244199A1 (en) 2002-07-01 2003-06-30 Material for sliding parts having self-lubricity and wire material for piston ring
EP03761840A EP1529852B1 (fr) 2002-07-01 2003-06-30 Materiau pour pieces coulissantes auto-lubrifiantes et materiau en fil pour segment de piston
US10/519,981 US20060048865A1 (en) 2002-07-01 2003-06-30 Material for sliding parts having self lubricity and wire material for piston ring

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JP2002191722 2002-07-01

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Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2007099968A1 (fr) * 2006-02-28 2007-09-07 Nippon Piston Ring Co., Ltd. Segment de piston
JP2008525630A (ja) * 2004-12-24 2008-07-17 マーレ ヴェンティルトリープ ゲゼルシャフト ミット ベシュレンクテル ハフツング 自動車内燃機関のターボチャージャのベーン支承リング
JP2012521488A (ja) * 2009-03-26 2012-09-13 フェデラル−モーグル ブルシェイド ゲーエムベーハー ピストンリングとシリンダーライナの製造用窒化可能な鋼組成物
CN103469108A (zh) * 2013-09-05 2013-12-25 无锡双友石化机械有限公司 扩径锥体及其制作工艺
JPWO2018056282A1 (ja) * 2016-09-20 2018-10-04 日立金属株式会社 摺動部品、摺動構造体および摺動構造体の摺動方法
JP6472938B1 (ja) * 2017-10-30 2019-02-20 Ｔｐｒ株式会社 圧力リング、内燃機関、圧力リング用線材および圧力リング用線材の製造方法
WO2019087562A1 (fr) * 2017-10-30 2019-05-09 Ｔｐｒ株式会社 Bague de pression, moteur à combustion interne, fil machine pour bague de pression, et procédé de fabrication de fil machine pour bague de pression

Families Citing this family (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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SE531889C2 (sv) * 2007-01-26 2009-09-01 Sandvik Intellectual Property Blyfritt automatstål och användning därav
JP2010031835A (ja) * 2008-06-23 2010-02-12 Nissan Motor Co Ltd 内燃機関用オイルリング及びピストン
BRPI0805606A2 (pt) * 2008-12-15 2010-09-14 Whirlpool S.A composição de materiais particulados para formação de produtos autolubrificantes em aço sinterizado, produto em aço sinterizado autolubrificante e processo de obtenção de produtos autolubrificantes em aço sinterizado
DE102009010727B3 (de) * 2009-02-26 2011-01-13 Federal-Mogul Burscheid Gmbh Stahlgusswerkstoffzusammensetzung zur Herstellung von Kolbenringen und Zylinderlaufbuchsen
CN101906597A (zh) * 2010-08-14 2010-12-08 武汉钢铁(集团)公司 一种环保型高性能石墨化易切削钢
WO2015117208A1 (fr) * 2014-02-07 2015-08-13 Mahle Metal Leve S/A Second segment de piston et piston automobile
CN107119224A (zh) * 2017-04-12 2017-09-01 滁州市东华模具制造有限公司 一种抗冷冲模具材料的制备方法
CN107419166A (zh) * 2017-07-04 2017-12-01 广东省材料与加工研究所 一种高强耐磨蚀合金钢材料及其制备方法
JP7292322B2 (ja) * 2021-04-12 2023-06-16 トクセン工業株式会社 オイルリング用線

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH10140293A (ja) * 1996-11-01 1998-05-26 Nippon Koshuha Steel Co Ltd 合金鋼およびその製造方法
US5908710A (en) * 1992-04-16 1999-06-01 Creusot Loire Industrie Process for manufacturing a clad sheet which includes an abrasion-resistant layer made of tool steel, and clad sheet obtained
US20020005616A1 (en) * 1999-06-25 2002-01-17 Hitachi Metals, Ltd. Self-lubricating piston ring material for internal combustion engine and piston ring

Family Cites Families (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2014440A (en) * 1928-01-13 1935-09-17 Gen Motors Corp Method of heat treating piston rings
DE1458487B1 (de) * 1963-08-24 1970-09-24 Schladitz, Hermann, 8000 München Verfahren zur pulvermetallurgischen Herstellung selbstschmierender, Trockenschmiermittel enthaltender Werkstoffe
AT287404B (de) * 1966-10-10 1971-01-25 Max Dr Ing Koehler Kolbenring und Verfahren zu seiner Herstellung
JPS60155645A (ja) * 1983-08-31 1985-08-15 Sumitomo Metal Ind Ltd デイスクブレ−キロ−タ用鋼
JPH04329850A (ja) * 1991-04-26 1992-11-18 Hitachi Metals Ltd 防振材料およびその製造方法
CN2114505U (zh) * 1992-03-16 1992-09-02 南通市化工机械厂 无泄漏自润滑磁力传动反应釜
EP0722796B1 (fr) * 1995-01-17 2001-09-19 Sumitomo Electric Industries, Ltd. Procédé pour la production des pièces frittées à base de fer traitées thermiquement
DE19654893C2 (de) * 1996-07-25 1999-06-10 Federal Mogul Burscheid Gmbh Kolbenringe von Verbrennungskraftmaschinen aus einer Gußeisenlegierung
US6139598A (en) * 1998-11-19 2000-10-31 Eaton Corporation Powdered metal valve seat insert
CN1272529A (zh) * 2000-05-30 2000-11-08 宝山钢铁股份有限公司 金属热加工用润滑剂

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5908710A (en) * 1992-04-16 1999-06-01 Creusot Loire Industrie Process for manufacturing a clad sheet which includes an abrasion-resistant layer made of tool steel, and clad sheet obtained
JPH10140293A (ja) * 1996-11-01 1998-05-26 Nippon Koshuha Steel Co Ltd 合金鋼およびその製造方法
US20020005616A1 (en) * 1999-06-25 2002-01-17 Hitachi Metals, Ltd. Self-lubricating piston ring material for internal combustion engine and piston ring

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP1529852A4 *

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2008525630A (ja) * 2004-12-24 2008-07-17 マーレ ヴェンティルトリープ ゲゼルシャフト ミット ベシュレンクテル ハフツング 自動車内燃機関のターボチャージャのベーン支承リング
WO2007099968A1 (fr) * 2006-02-28 2007-09-07 Nippon Piston Ring Co., Ltd. Segment de piston
US8240676B2 (en) 2006-02-28 2012-08-14 Nippon Piston Ring Co., Ltd. Piston ring
JP2012521488A (ja) * 2009-03-26 2012-09-13 フェデラル−モーグル ブルシェイド ゲーエムベーハー ピストンリングとシリンダーライナの製造用窒化可能な鋼組成物
CN103469108A (zh) * 2013-09-05 2013-12-25 无锡双友石化机械有限公司 扩径锥体及其制作工艺
JPWO2018056282A1 (ja) * 2016-09-20 2018-10-04 日立金属株式会社 摺動部品、摺動構造体および摺動構造体の摺動方法
JP6472938B1 (ja) * 2017-10-30 2019-02-20 Ｔｐｒ株式会社 圧力リング、内燃機関、圧力リング用線材および圧力リング用線材の製造方法
WO2019087562A1 (fr) * 2017-10-30 2019-05-09 Ｔｐｒ株式会社 Bague de pression, moteur à combustion interne, fil machine pour bague de pression, et procédé de fabrication de fil machine pour bague de pression

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AU2003244199A1 (en) 2004-01-19
CN1665950A (zh) 2005-09-07
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US20060048865A1 (en) 2006-03-09
EP1529852B1 (fr) 2008-12-31
CN1327025C (zh) 2007-07-18
EP1529852A1 (fr) 2005-05-11
JP4273462B2 (ja) 2009-06-03
DE60325602D1 (de) 2009-02-12
JPWO2004003246A1 (ja) 2005-10-27
KR20050014896A (ko) 2005-02-07
KR100701812B1 (ko) 2007-04-02

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