WO2022219854A1 - オイルリング用線 - Google Patents
オイルリング用線 Download PDFInfo
- Publication number
- WO2022219854A1 WO2022219854A1 PCT/JP2021/048637 JP2021048637W WO2022219854A1 WO 2022219854 A1 WO2022219854 A1 WO 2022219854A1 JP 2021048637 W JP2021048637 W JP 2021048637W WO 2022219854 A1 WO2022219854 A1 WO 2022219854A1
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- WO
- WIPO (PCT)
- Prior art keywords
- mass
- wire
- less
- oil ring
- ring
- Prior art date
Links
- 229910000851 Alloy steel Inorganic materials 0.000 claims abstract description 39
- 239000000463 material Substances 0.000 claims abstract description 17
- 239000012535 impurity Substances 0.000 claims abstract description 12
- 238000000137 annealing Methods 0.000 claims description 21
- 238000010791 quenching Methods 0.000 claims description 16
- 230000000171 quenching effect Effects 0.000 claims description 16
- 229910001566 austenite Inorganic materials 0.000 claims description 15
- 238000005097 cold rolling Methods 0.000 claims description 9
- 238000000034 method Methods 0.000 claims description 9
- 239000013078 crystal Substances 0.000 claims description 8
- 238000004519 manufacturing process Methods 0.000 claims description 8
- 238000005496 tempering Methods 0.000 claims description 7
- 238000005491 wire drawing Methods 0.000 claims description 6
- 150000001247 metal acetylides Chemical class 0.000 abstract description 16
- 229910052799 carbon Inorganic materials 0.000 abstract description 3
- 229910052804 chromium Inorganic materials 0.000 abstract description 3
- 229910052802 copper Inorganic materials 0.000 abstract description 3
- 229910052748 manganese Inorganic materials 0.000 abstract description 3
- 229910052759 nickel Inorganic materials 0.000 abstract description 3
- 229910052710 silicon Inorganic materials 0.000 abstract description 3
- 229910052720 vanadium Inorganic materials 0.000 abstract description 2
- 239000003921 oil Substances 0.000 description 98
- 208000035193 Ring chromosome 10 syndrome Diseases 0.000 description 46
- 238000005121 nitriding Methods 0.000 description 22
- 238000010438 heat treatment Methods 0.000 description 19
- 230000002093 peripheral effect Effects 0.000 description 14
- 239000011651 chromium Substances 0.000 description 13
- 239000010949 copper Substances 0.000 description 11
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 11
- 239000011572 manganese Substances 0.000 description 10
- 239000011248 coating agent Substances 0.000 description 9
- 238000000576 coating method Methods 0.000 description 9
- 238000010622 cold drawing Methods 0.000 description 7
- 239000011159 matrix material Substances 0.000 description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 6
- 238000005240 physical vapour deposition Methods 0.000 description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- 238000002485 combustion reaction Methods 0.000 description 4
- 229910000734 martensite Inorganic materials 0.000 description 4
- 239000002245 particle Substances 0.000 description 4
- 238000007747 plating Methods 0.000 description 4
- 230000000717 retained effect Effects 0.000 description 4
- 229910000975 Carbon steel Inorganic materials 0.000 description 3
- 239000010962 carbon steel Substances 0.000 description 3
- 239000010935 stainless steel Substances 0.000 description 3
- 229910001220 stainless steel Inorganic materials 0.000 description 3
- 229910000831 Steel Inorganic materials 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 150000004767 nitrides Chemical class 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- 230000001629 suppression Effects 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 238000007733 ion plating Methods 0.000 description 1
- 230000001788 irregular Effects 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000001000 micrograph Methods 0.000 description 1
- 239000003129 oil well Substances 0.000 description 1
- 238000013021 overheating Methods 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- 239000002699 waste material Substances 0.000 description 1
Images
Classifications
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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
- 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
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/06—Surface hardening
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/32—Soft annealing, e.g. spheroidising
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
-
- 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
-
- 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
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
- C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
-
- 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
-
- 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
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/003—Cementite
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of 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
- C22C38/18—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
Definitions
- the present invention relates to a wire for an oil ring attached to a piston of an internal combustion engine.
- the present invention relates to wires suitable for two-piece combination oil rings.
- An internal combustion engine has a cylinder, a piston, a pressure ring and an oil ring.
- a pressure ring and an oil ring are attached to the piston.
- Pressure rings and oil rings are collectively referred to as piston rings.
- An example of a piston ring is disclosed in JP-A-2008-50649.
- the movement of the piston also moves the oil ring inside the cylinder.
- the oil ring scrapes off oil adhering to the inner peripheral surface by this movement. This oil returns to the oil pan.
- Oil rings are roughly classified into two-piece type combination oil rings and three-piece type combination oil rings.
- a two-piece combination oil ring has a main ring (referred to as the "body") and a coil expander.
- the main ring has a pair of rails. The outer peripheral surface of each rail rubs against the inner peripheral surface of the cylinder.
- a main ring whose material is stainless steel is widespread. This main ring is subjected to nitriding treatment. The surface of this primary ring is hard. Nitriding contributes to the wear resistance of the main ring.
- Main rings whose material is carbon steel or low-alloy steel are prevalent. Carbon steel and low alloy steel are excellent in workability. This main ring can therefore be easily obtained.
- This main ring has a hard coating. This hard coating can be formed by plating (or coating). The hard coating contributes to the wear resistance of the main ring.
- the main ring whose material is stainless steel, has a high material cost. Since stainless steel is inferior in workability, it is not easy to obtain a main ring having a complicated shape.
- the main ring whose material is general carbon steel or low alloy steel, is not suitable for nitriding treatment. Therefore, this main ring is plated or coated as described above. Plating requires costs such as waste liquid treatment. The coating requires a heating step, which causes softening of the primary ring.
- An object of the present invention is to provide a wire from which a low-cost oil ring with excellent wear resistance can be obtained.
- the material of the oil ring wire according to the present invention is alloy steel.
- This alloy steel C 0.50% by mass or more and 0.65% by mass or less Si: 1.60% by mass or more and 2.30% by mass or less
- Mn 0.60% by mass or more and 1.10% by mass or less
- Cr 0.75% by mass or more 1.15% by mass or less
- Ni 0.18% by mass or more and 0.45% by mass or less
- V 0.05% by mass or more and 0.15% by mass or less
- Cu 0.15% by mass or less Including unavoidable impurities.
- the area ratio of carbide in this oil ring wire is more than 6.0% and not more than 10.0%.
- the Vickers hardness of this oil ring wire is preferably 510 or more and 650 or less.
- the oil ring wire can have a body and a pair of rails. Each rail protrudes from the body.
- the rail has a tip. Preferably, the width of the tip is 0.10 mm or less.
- the grain size number of the prior austenite crystals of this oil ring wire is 9.0 or more.
- the method for manufacturing an oil ring wire according to the present invention includes: (1) The material is C: 0.50% by mass or more and 0.65% by mass or less Si: 1.60% by mass or more and 2.30% by mass or less Mn: 0.60% by mass or more and 1.10% by mass or less Cr: 0.75% by mass or more 1.15% by mass or less Ni: 0.18% by mass or more and 0.45% by mass or less V: 0.05% by mass or more and 0.15% by mass or less Cu: 0.15% by mass or less Alloy steel containing unavoidable impurities
- an oil ring wire having an area ratio of carbide of more than 6.0% and not more than 10.0% can be obtained.
- the alloy steel which is the material of the oil ring wire according to the present invention, is inexpensive. This alloy steel has excellent workability. Furthermore, since this oil ring wire is suitable for nitriding treatment, the main ring or the like obtained from this wire does not require plating. Oil rings can be obtained from this line at low cost.
- This oil ring wire contains carbide.
- This carbide contributes to the hardness of the main ring and the like.
- the main ring and the like containing this carbide are excellent in softening resistance.
- a main ring or the like obtained from this wire through heat treatment has high hardness.
- This oil ring has excellent wear resistance.
- FIG. 1 is a perspective view showing part of an oil ring wire according to one embodiment of the present invention.
- FIG. 2 is an enlarged cross-sectional view taken along line II--II of FIG.
- FIG. 3 is a flow chart showing an example of a method for manufacturing the oil ring wire of FIG. 4 is a perspective view showing a main ring obtained from the oil ring wire of FIG. 1.
- FIG. 5 is an enlarged cross-sectional view taken along line VV of FIG. 4.
- FIG. FIG. 6 is a graph showing the Vickers hardness of the nitride layer of the main ring of FIG. 7 is a cross-sectional view showing a part of an oil ring including the main ring of FIG. 4;
- FIG. FIG. 8 is a micrograph showing the metallographic structure of the oil ring wire according to Example 1 of the present invention.
- the oil ring wire 2 is shown in FIGS.
- the cross-sectional shape of this oil ring wire 2 is not circular. In other words, the oil ring wire 2 has an irregular shape.
- this oil ring wire 2 has a body 4 and a pair of rails 6 . Each rail 6 has a tip 8 .
- the material of the oil ring wire 2 is alloy steel.
- This alloy steel C 0.50% by mass or more and 0.65% by mass or less Si: 1.60% by mass or more and 2.30% by mass or less
- Mn 0.60% by mass or more and 1.10% by mass or less
- Cr 0.75% by mass or more 1.15% by mass or less
- Ni 0.18% by mass or more and 0.45% by mass or less
- V 0.05% by mass or more and 0.15% by mass or less
- Cu 0.15% by mass or less.
- the balance is Fe and incidental impurities.
- the amount of alloying elements contained in this alloy steel is relatively low.
- the material of the oil ring wire 2 is low alloy steel. This low alloy steel is inexpensive.
- FIG. 3 is a flow chart showing an example of a method for manufacturing the oil ring wire 2 of FIG.
- a basic wire is prepared (STEP 1).
- This original wire is obtained through processes such as steelmaking, refining, casting, hot rolling, and annealing.
- the cross-sectional shape of this primitive line is a circle.
- the diameter of this circle is, for example, 6.4 mm.
- This wire is subjected to cold drawing (STEP 2).
- the original wire is gradually made thinner and longer.
- the cross-sectional shape of the wire after cold drawing (STEP 2) is a circle.
- the diameter of this wire is, for example, 4.5 mm.
- Patenting is a heat treatment that cools a wire heated to the austenite region to obtain a fine pearlite structure.
- the patenting restores the ductility of the wire that was damaged by the cold wire drawing (STEP 2).
- Cold wire drawing (STEP2) and patenting (STEP3) may be omitted.
- the wire may be subjected to spheroidizing annealing.
- This wire is further subjected to cold drawing (STEP 4).
- cold drawing By this cold drawing, the wire is gradually made thinner and longer.
- the cross-sectional shape of the wire after cold drawing (STEP 4) is a circle.
- the diameter of this wire is, for example, 3.0 mm. Patenting (STEP 3) and cold drawing (STEP 4) may be repeated as necessary.
- This wire is subjected to spheroidizing annealing (STEP 5) to obtain a fine wire.
- the spheroidizing annealing produces spheroidal carbides in the fine wires.
- the spheroidizing annealing restores the ductility of the thin wire that was damaged by the cold wire drawing (STEP 4).
- the holding temperature in the spheroidizing annealing (STEP 5) is preferably 700°C or higher, more preferably 730°C or higher, and particularly preferably 750°C or higher.
- the holding time in spheroidizing annealing (STEP 5) is preferably 4.0 hours or longer, more preferably 4.3 hours or longer, and particularly preferably 4.5 hours or longer.
- This thin wire is subjected to cold rolling (STEP 6).
- a profiled wire is obtained by this cold rolling.
- the cross-sectional shape of the deformed wire is not circular.
- the thickness is 2.2 mm and the width is 2.2 mm.
- This deformed wire is subjected to spheroidizing annealing (STEP 7).
- spheroidizing annealing (STEP7), spheroidal carbides generated in the previous spheroidizing annealing (STEP5) grow. Furthermore, this spheroidizing annealing (STEP 7) produces new spheroidal carbides.
- the spheroidizing annealing (STEP 7) restores the ductility of the deformed wire that was damaged by the cold rolling (STEP 6).
- the holding temperature in the spheroidizing annealing (STEP 7) is preferably 700°C or higher, more preferably 730°C or higher, and 750°C. The above are particularly preferred. From the same point of view, the holding time in spheroidizing annealing (STEP 7) is preferably 4.0 hours or longer, more preferably 4.3 hours or longer, and particularly preferably 4.5 hours or longer.
- This wire is further cold rolled (STEP 8).
- This cold rolling changes the cross section of the shaped wire.
- the profile wire after cold rolling (STEP 8) has a thickness of 2.0 mm and a width of 2.0 mm.
- Spheroidizing annealing (STEP 7) and cold rolling (STEP 8) may be repeated as necessary.
- This deformed wire is quenched.
- the deformed wire is heated (STEP 9). During this heating, the temperature of the profile wire reaches the austenite region.
- this shaped wire is quenched (STEP 10).
- the profile wire is cooled in oil.
- the profile wire after quenching has a martensite structure.
- This deformed wire is tempered. In tempering, first, the deformed wire is heated (STEP 11). Next, this shaped wire is cooled (STEP 12). By tempering, the oil ring wire 2 shown in FIG. 1 is obtained.
- a coil is obtained by coiling the oil ring wire 2 .
- This coil is subjected to strain relief heat treatment. Further, this coil is subjected to nitriding treatment. In nitriding, the coil is held in a high temperature (eg, 500° C.) environment.
- This nitriding treatment yields the primary ring 10 shown in FIGS.
- this main ring 10 has, near its surface, a hard layer 12 obtained by nitriding.
- This hard layer 12 exists over the entire surface of the main ring 10 .
- This hard layer 12 contains nitride.
- the hard layer 12 may be formed by physical vapor deposition, ion plating, or the like instead of the nitriding treatment.
- this main ring 10 has a pair of outer peripheral surfaces 14 .
- FIG. 6 shows the relationship between the Vickers hardness (load: 50 gf) and the depth from the surface of the main ring 10 after nitriding.
- the Vickers hardness required for the main ring 10 is 700 or higher.
- the main ring 10 obtained from the oil ring wire 2 according to the present invention has a Vickers hardness of 700 or more from the zero depth position to the 70 ⁇ m depth position. has been achieved.
- the oil ring wire 2 according to the present invention is more suitable for nitriding than low alloy steel (hard steel wire, etc.).
- FIG. 7 is a cross-sectional view showing part of the oil ring 16 including the main ring 10 of FIG.
- This oil ring 16 has a main ring 10 and a coil expander 18 .
- This oil ring 16 is called a two-piece combined oil ring.
- Reference numeral 20 in FIG. 7 represents the inner peripheral surface of the cylinder.
- Each outer peripheral surface 14 of the primary ring 10 abuts an inner peripheral surface 20 .
- the shape of the tip portion 8 of the oil ring wire 2 shown in FIG. 2 is reflected on the outer peripheral surface 14 of the main ring 10 shown in FIG.
- the material of the oil ring wire 2 is low alloy steel. This low alloy steel has excellent workability. Therefore, the tip portion 8 can be easily formed by cold rolling (STEP 6, STEP 8).
- the main ring 10 obtained from this oil ring wire 2 does not require extensive finishing.
- the main ring 10 can be obtained from this oil ring wire 2 at low cost.
- the two corners of the tip 8 are rounded.
- the arrow W in FIG. 2 indicates the width of the tip portion 8 .
- Width W is the distance between two corners assuming they are not rounded.
- the width W is preferably 0.10 mm or less.
- a main ring 10 having a small width of the outer peripheral surface 14 can be obtained from the oil ring wire 2 having a width W of 0.10 mm or less. This main ring 10 abuts against the inner peripheral surface 20 of the cylinder with great pressure. An oil ring 16 having this main ring 10 scrapes oil well. It is difficult to process a raw wire made of high alloy steel into an oil ring wire 2 having a width W of 0.10 mm or less.
- the material of the original wire that is, low-alloy steel
- this main ring 10 alloying elements enable nitriding treatment. Therefore, this main ring 10 does not require plating. This primary ring 10 can be obtained at low cost.
- the area ratio Ps of the spheroidal carbides in the oil ring wire 2 has a negative correlation with the heat energy given to the deformed wire in the heating for quenching (STEP 9). Therefore, the area ratio Ps has a negative correlation with the grain size of the deformed wire after quenching, and has a positive correlation with the grain boundary area.
- the area ratio Ps of the carbide in the oil ring wire 2 is preferably more than 6.0%, more preferably 6.5% or more, and particularly preferably 7.0% or more.
- the area ratio Ps of the carbide in the oil ring wire 2 is preferably 10.0% or less, more preferably 9.5% or less, and particularly preferably 9.0% or less.
- the image analysis software "Image J" is used to measure the area ratio Ps of carbide.
- a cross-section of the oil ring wire 2 is photographed with a scanning electron microscope to obtain an SEM photograph with a magnification of 3000 times.
- the image file of this photograph is binarized by the image analysis software, and the area of the carbide particles and other areas are color-coded.
- the area of each carbide grain is calculated.
- a circle having an area equal to this area is assumed, and the diameter of this circle is taken as the diameter of this particle.
- the diameter and number of carbides with a diameter of 0.05 ⁇ m or more are histogrammed. Carbides less than 0.05 ⁇ m in diameter are excluded from the count.
- the total area of carbides with a diameter of 0.05 ⁇ m or more is calculated.
- the ratio of this total area to the total area of the photograph is the area ratio Ps.
- the area ratio Ps is the ratio of the area occupied by granular carbides (including spherical carbides).
- the temperature in the heating for quenching is preferably 950°C or higher, and particularly preferably 980°C or higher. This temperature is preferably 1050° C. or less from the viewpoint of achieving an area ratio Ps that is not too small.
- the deformed wire In quenching, the deformed wire is heated to a high temperature (STEP 9) and then rapidly cooled (STEP 10).
- the metallographic structure of the profile wire under high temperature is austenite. This metallographic structure has austenitic grains. This profiled wire is quenched. Rapid cooling transforms the metal structure to martensite. Due to this rapid cooling, the compound is preferentially precipitated from the grain boundaries of the austenite crystal grains. Therefore, austenite crystals before quenching (old austenite crystals) affect the structure of martensite. Evidence of prior austenite crystals can be observed in the martensite.
- the grain size number of the prior austenite crystals in the oil ring wire 2 is preferably 9.0 or more. In other words, the prior austenite crystals are fine.
- the main ring 10 obtained from this oil ring wire 2 has excellent fatigue resistance. From this point of view, the particle size number is more preferably 9.5 or higher, and particularly preferably 10.0 or higher.
- the particle size number is measured according to the provisions of "JIS G 0551:2020". A 100 ⁇ magnification photograph obtained by microscopic observation of the cross-section shown in FIG. A grain size number of 9.0 or more can be achieved by suppressing overheating during quenching.
- the Vickers hardness Hv of the oil ring wire 2 is preferably 510 or more. Sufficient hardness can be maintained even when the oil ring wire 2 is subjected to heat treatment or nitriding treatment. A main ring 10 having excellent wear resistance can be obtained from this oil ring wire 2 . From this point of view, the Vickers hardness is more preferably 530 or higher, particularly preferably 560 or higher. From the viewpoint of ease of coiling, the Vickers hardness of the oil ring wire 2 is preferably 650 or less. Vickers hardness is measured according to the provisions of "JIS Z 2244". A load of 10 kgf is applied and the Vickers hardness is measured.
- the high Vickers hardness of conventional high alloy steels that can be nitrided causes breakage during coiling.
- the low-alloy steel of the oil ring wire 2 according to the present invention is excellent in workability although nitriding treatment is possible.
- This oil ring wire 2 can achieve both high Vickers hardness and workability. From this oil ring wire 2, a main ring 10 having excellent wear resistance can be obtained at low cost.
- PVD physical vapor deposition
- Physical vapor deposition forms a hard coating. This coating is formed in the vicinity of the outer peripheral surface 14 . This coating can suppress wear of the main ring 10 caused by friction with the inner peripheral surface 20 of the cylinder. No film is formed on the remaining portion of the surface of the main ring 10 .
- the main ring 10 contacts the piston at points where it does not have a coating.
- the main ring 10 has undergone strain relief heat treatment. Further, the primary ring 10 has undergone physical vapor deposition. Since the oil ring wire 2 according to the present invention has excellent softening resistance, the main ring 10 has sufficient hardness even after undergoing these thermal histories.
- C Carbon (C) C dissolves in the matrix.
- An appropriate amount of C contributes to the hardness and fatigue resistance of the oil ring wire 2 .
- C produces carbides. This carbide contributes to the wear resistance of the oil ring wire 2 .
- the C content is preferably 0.50% by mass or more, more preferably 0.53% by mass or more, and particularly preferably 0.55% by mass or more. Excess C impairs the cold workability of the alloy steel. From the viewpoint of cold workability, the C content is preferably 0.65% by mass or less.
- Si contributes to the high-temperature strength and softening resistance of the oil ring wire 2 . From these points of view, the Si content is preferably 1.60% by mass or more, more preferably 1.80% by mass or more, and particularly preferably 2.00% by mass or more. Excess Si impairs the cold workability, toughness and hardenability of the alloy steel. From these points of view, the Si content is preferably 2.30% by mass or less.
- Mn functions as a deoxidizing agent during melting of low alloy steel. Furthermore, Mn suppresses the adverse effects of S, which is an impurity. From these points of view, the Mn content is preferably 0.60% by mass or more, more preferably 0.80% by mass or more, and particularly preferably 0.90% by mass or more. From the viewpoint of the cold workability of the alloy steel, the Mn content is preferably 1.10% by mass or less.
- [Chromium (Cr)] Cr combines with nitrogen in the nitriding process. Cr enables the nitriding treatment of the oil ring wire 2 .
- the hard layer 12 obtained in nitriding contributes to the wear resistance of the main ring 10 .
- Cr further combines with C to form carbides. This carbide contributes to the wear resistance of the main ring 10 .
- the Cr content is preferably 0.75% by mass or more, more preferably 0.85% by mass or more, and particularly preferably 0.90% by mass or more. Excess Cr impairs the cold workability of the alloy steel. Excessive Cr further causes breakage of the oil ring wire 2 during coiling. From the viewpoint of cold workability and breakage suppression, the Cr content is preferably 1.15% by mass or less.
- Nickel (Ni) Ni dissolves in the matrix and contributes to the toughness of the oil ring wire 2 .
- the Ni content is preferably 0.18% by mass or more, more preferably 0.25% by mass or more, and particularly preferably 0.30% by mass or more.
- Excessive Ni produces retained austenite in the oil ring wire 2 after quenching. This retained austenite leads to a low elevation of the primary ring 10 . This retained austenite further changes the dimensions of the primary ring 10 by aging. From the viewpoint of suppressing retained austenite, the Ni content is preferably 0.45% by mass or less.
- V combines with nitrogen in the nitriding process.
- V enables the nitriding treatment of the oil ring wire 2 .
- the hard layer 12 obtained in nitriding contributes to the wear resistance of the main ring 10 .
- V further contributes to refinement of the metal structure.
- the V content is preferably 0.05% by mass or more, more preferably 0.08% by mass or more, and particularly preferably 0.10% by mass or more. From the viewpoint of the cold workability and hot workability of the alloy steel, the V content is preferably 0.15% by mass or less.
- Cu contributes to toughness during cold working.
- the Cu content is preferably 0.05% by mass or more, more preferably 0.08% by mass or more, and particularly preferably 0.10% by mass or more.
- the Cu content is preferably 0.15% by mass or less.
- Cu is not an essential element. Therefore, the Cu content may be substantially zero.
- Fe is the main component of low-alloy steel. Fe is the base metal of the matrix. This low alloy steel has excellent toughness.
- the Fe content is preferably 85% by mass or more, more preferably 90% by mass or more, and particularly preferably 93% by mass or more.
- Low alloy steel may contain impurities.
- a typical impurity is P. P segregates at grain boundaries. P impairs the toughness of alloy steel. From the viewpoint of toughness, the P content is preferably 0.02% by mass or less.
- Another typical impurity is S. S combines with other elements to form inclusions. S impairs the toughness of alloy steel. From the viewpoint of toughness, the S content is preferably 0.02% by mass or less.
- Example 1 An oil ring wire of Example 1 was obtained by the method shown in FIG. The heating temperature during quenching was 980°C. The tempering temperature was appropriately adjusted so as to obtain the desired hardness.
- the material of this oil ring wire was low alloy steel. This low alloy steel contains 0.59 wt% C, 2.05 wt% Si, 0.76 wt% Mn, 1.00 wt% Cr, 0.22 wt% Ni, 0.09 wt% % V and 0.01 wt % Cu. The balance was Fe and unavoidable impurities.
- the metallographic structure of this oil ring wire is shown in FIG. The area ratio Ps of this oil ring wire was 6.4%. The Vickers hardness of this oil ring wire (load: 10 kgf) was 589.
- Heat treatment A coil was formed from the oil ring wire, and the coil was held at a temperature of 450° C. for 30 minutes and then slowly cooled. This heat treatment condition corresponds to the condition of stress relief heat treatment that is generally performed in the manufacture of the main ring. The Vickers hardness (load: 10 kgf) of the coil after this heat treatment was measured. The results are shown in Table 1 below.
- the Vickers hardness required for the main ring is 450 or more. As shown in Table 1, the oil ring wire according to each example has a Vickers hardness exceeding 450 after heat treatment. From this evaluation result, the superiority of the present invention is clear.
- the oil ring wire according to the present invention can be used as a material for piston rings of various internal combustion engines.
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Abstract
Description
C:0.50質量%以上0.65質量%以下
Si:1.60質量%以上2.30質量%以下
Mn:0.60質量%以上1.10質量%以下
Cr:0.75質量%以上1.15質量%以下
Ni:0.18質量%以上0.45質量%以下
V:0.05質量%以上0.15質量%以下
Cu:0.15質量%以下
及び
不可避的不純物
を含む。このオイルリング用線の、炭化物の面積率は、6.0%を超えて10.0%以下である。
(1)その材質が、
C:0.50質量%以上0.65質量%以下
Si:1.60質量%以上2.30質量%以下
Mn:0.60質量%以上1.10質量%以下
Cr:0.75質量%以上1.15質量%以下
Ni:0.18質量%以上0.45質量%以下
V:0.05質量%以上0.15質量%以下
Cu:0.15質量%以下
及び
不可避的不純物
を含む合金鋼である原線に、冷間伸線及び球状化焼鈍を施して、細線を得る工程、
(2)この細線に、冷間圧延及び球状化焼鈍を施して、異形線を得る工程、
並びに
(3)この異形線に焼入れ及び焼戻しを施す工程
を含む。この製造方法により、炭化物の面積率が6.0%を超えて10.0%以下であるオイルリング用線が得られる。
C:0.50質量%以上0.65質量%以下
Si:1.60質量%以上2.30質量%以下
Mn:0.60質量%以上1.10質量%以下
Cr:0.75質量%以上1.15質量%以下
Ni:0.18質量%以上0.45質量%以下
V:0.05質量%以上0.15質量%以下
及び
Cu:0.15質量%以下
を含んでいる。好ましくは、残部はFe及び不可避的不純物である。この合金鋼に含まれる合金元素の量は、比較的少ない。このオイルリング用線2の材質は、低合金鋼である。この低合金鋼は、安価である。
この製造方法では、まず、原線(Basic Wire)が準備される(STEP1)。この原線は、製鋼、精錬、鋳造、熱間圧延、焼鈍し等の工程を経て得られる。この原線の断面形状は、円である。この円の直径は、例えば6.4mmである。
Cは、マトリックスに固溶する。適量なCは、オイルリング用線2の硬度及び耐疲労性に寄与する。さらにCは、炭化物を生成させる。この炭化物は、オイルリング用線2の耐摩耗性に寄与する。これらの観点から、Cの含有率は0.50質量%以上が好ましく、0.53質量%以上がより好ましく、0.55質量%以上が特に好ましい。過剰のCは、合金鋼の冷間加工性を損なう。冷間加工性の観点から、Cの含有率は0.65質量%以下が好ましい。
Siは、オイルリング用線2の高温強度及び軟化抵抗に寄与する。これらの観点から、Siの含有率は1.60質量%以上が好ましく、1.80質量%以上がより好ましく、2.00質量%以上が特に好ましい。過剰のSiは、合金鋼の冷間加工性、靱性及び焼入れ性を損なう。これらの観点から、Siの含有率は2.30質量%以下が好ましい。
Mnは、低合金鋼の溶製時に、脱酸剤として機能する。さらにMnは、不純物であるSの悪影響を抑制する。これらの観点から、Mnの含有率は0.60質量%以上が好ましく、0.80質量%以上がより好ましく、0.90質量%以上が特に好ましい。合金鋼の冷間加工性の観点から、Mnの含有率は1.10質量%以下が好ましい。
Crは、窒化処理において窒素と結合する。Crは、オイルリング用線2の窒化処理を可能とせしめる。窒化処理において得られた硬質層12は、主リング10の耐摩耗性に寄与する。Crはさらに、Cと結合して炭化物を生成させる。この炭化物は、主リング10の耐摩耗性に寄与する。これらの観点から、Crの含有率は0.75質量%以上が好ましく、0.85質量%以上がより好ましく、0.90質量%以上が特に好ましい。過剰のCrは、合金鋼の冷間加工性を阻害する。過剰のCrはさらに、コイリングのときのオイルリング用線2の折損を招来する。冷間加工性及び折損抑制の観点から、Crの含有率は1.15質量%以下が好ましい。
Niは、マトリックスに固溶し、オイルリング用線2の靱性に寄与する。この観点から、Niの含有率は0.18質量%以上が好ましく、0.25質量%以上がより好ましく、0.30質量%以上が特に好ましい。過剰のNiは、焼入れ後のオイルリング用線2に残留オーステナイトを生成させる。この残留オーステナイトは、主リング10の低高度を招来する。この残留オーステナイトはさらに、時効によって主リング10の寸法を変化させる。残留オーステナイトの抑制の観点から、Niの含有率は0.45質量%以下が好ましい。
Vは、窒化処理において窒素と結合する。Vは、オイルリング用線2の窒化処理を可能とせしめる。窒化処理において得られた硬質層12は、主リング10の耐摩耗性に寄与する。Vはさらに、金属組織の微細化に寄与する。これらの観点から、Vの含有率は0.05質量%以上が好ましく、0.08質量%以上がより好ましく、0.10質量%以上が特に好ましい。合金鋼の冷間加工性及び熱間加工性の観点から、Vの含有率は0.15質量%以下が好ましい。
Cuは、冷間加工時の靱性に寄与する。この観点から、Cuの含有率は0.05質量%以上が好ましく、0.08質量%以上がより好ましく、0.10質量%以上が特に好ましい。合金鋼の熱間加工性の観点から、Cuの含有率は0.15質量%以下が好ましい。Cuは、必須の元素ではない。従って、Cuの含有率が実質的にゼロでもよい。
Feは、低合金鋼の主成分である。Feは、マトリックスのベース金属である。この低合金鋼は、強靱性に優れる。Feの含有率は85質量%以上が好ましく、90質量%以上がより好ましく、93質量%以上が特に好ましい。
低合金鋼は、不純物を含みうる。典型的な不純物は、Pである。Pは、結晶粒界に偏析する。Pは、合金鋼の靱性を阻害する。靱性の観点から、Pの含有率は0.02質量%以下が好ましい。他の典型的な不純物は、Sである。Sは、他の元素と結合して介在物を形成する。Sは、合金鋼の靱性を阻害する。靱性の観点から、Sの含有率は0.02質量%以下が好ましい。
図3に示された方法にて、実施例1のオイルリング用線を得た。焼入れ時の加熱温度は、980℃であった。焼戻し温度は、好ましい硬さが得られるよう、適宜調整した。このオイルリング用線の材質は、低合金鋼であった。この低合金鋼は、0.59質量%のC、2.05質量%のSi、0.76質量%のMn、1.00質量%のCr、0.22質量%のNi、0.09質量%のV、及び0.01質量%のCuを含んでいた。残部は、Fe及び不可避的不純物であった。このオイルリング用線の金属組織が、図8に示されている。このオイルリング用線の面積率Psは、6.4%であった。このオイルリング用線のビッカース硬さ(荷重:10kgf)は、589であった。
焼入れ温度を下記の表1に示される通りとして、実施例2及び3並びに比較例1及び2のオイルリング用線を得た。
オイルリング用線からコイルを形成し、このコイルを450℃の温度下に30分間保持した後、徐冷した。この熱処理条件は、主リングの製造において一般的になされている歪取熱処理の条件に相当する。この熱処理後のコイルのビッカース硬さ(荷重:10kgf)を、測定した。この結果が、下記の表1に示されている。
4・・・ボディ
6・・・レール
8・・・先端部
10・・・主リング
12・・・硬質層
14・・・外周面
16・・・オイルリング
18・・・コイルエキスパンダー
20・・・シリンダーの内周面
Claims (5)
- その材質が合金鋼であり、
上記合金鋼が、
C:0.50質量%以上0.65質量%以下
Si:1.60質量%以上2.30質量%以下
Mn:0.60質量%以上1.10質量%以下
Cr:0.75質量%以上1.15質量%以下
Ni:0.18質量%以上0.45質量%以下
V:0.05質量%以上0.15質量%以下
Cu:0.15質量%以下
及び
不可避的不純物
を含んでおり、
炭化物の面積率が6.0%を超えて10.0%以下であるオイルリング用線。 - ビッカース硬さが510以上650以下である、請求項1に記載のオイルリング用線。
- ボディと、一対のレールとを有しており、
それぞれのレールが、上記ボディから突出しており、かつ先端部を有しており、
上記先端部の幅が0.10mm以下である請求項1又は2に記載のオイルリング用線。 - 旧オーステナイト結晶の粒度番号が9.0以上である請求項1から3のいずれかに記載のオイルリング用線。
- (1)その材質が、
C:0.50質量%以上0.65質量%以下
Si:1.60質量%以上2.30質量%以下
Mn:0.60質量%以上1.10質量%以下
Cr:0.75質量%以上1.15質量%以下
Ni:0.18質量%以上0.45質量%以下
V:0.05質量%以上0.15質量%以下
Cu:0.15質量%以下
及び
不可避的不純物
を含む合金鋼である原線に、冷間伸線及び球状化焼鈍を施して、細線を得る工程、
(2)上記細線に、冷間圧延及び球状化焼鈍を施して、異形線を得る工程、
並びに
(3)上記異形線に焼入れ及び焼戻しを施す工程
を備えた、炭化物の面積率が6.0%を超えて10.0%以下であるオイルリング用線の製造方法。
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US18/274,763 US20240026972A1 (en) | 2021-04-12 | 2021-12-27 | Oil ring wire |
CN202180094895.8A CN116897212A (zh) | 2021-04-12 | 2021-12-27 | 油环用线 |
KR1020237026521A KR20230128362A (ko) | 2021-04-12 | 2021-12-27 | 오일 링용 선 |
EP21937047.5A EP4276203A1 (en) | 2021-04-12 | 2021-12-27 | Oil ring wire |
MX2023009157A MX2023009157A (es) | 2021-04-12 | 2021-12-27 | Alambre de anillo de aceite. |
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EP (1) | EP4276203A1 (ja) |
JP (1) | JP7297808B2 (ja) |
KR (1) | KR20230128362A (ja) |
CN (1) | CN116897212A (ja) |
MX (1) | MX2023009157A (ja) |
TW (1) | TWI800200B (ja) |
WO (1) | WO2022219854A1 (ja) |
Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
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US5944920A (en) * | 1996-04-10 | 1999-08-31 | Hitachi Metals, Ltd. | Piston ring material excellent in workability |
JP2008050649A (ja) | 2006-08-24 | 2008-03-06 | Tokusen Kogyo Co Ltd | ピストンリング及びその製造方法 |
JP2010054039A (ja) * | 2008-08-29 | 2010-03-11 | Nippon Piston Ring Co Ltd | 内燃機関用オイルリング |
JP2015108417A (ja) * | 2013-12-05 | 2015-06-11 | 株式会社リケン | 大型ピストンリング及びその素材並びにそれらの製造方法。 |
Family Cites Families (5)
Publication number | Priority date | Publication date | Assignee | Title |
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EP1063454B1 (en) * | 1999-06-25 | 2006-04-19 | Hitachi Metals, Ltd. | Self-lubricating piston ring material for internal combustion engine and piston ring |
CN100535423C (zh) * | 2003-03-31 | 2009-09-02 | 日立金属株式会社 | 内燃机用活塞及其制造方法 |
EP2011892A1 (en) * | 2006-04-20 | 2009-01-07 | Hitachi Metals, Limited | Piston ring material for internal combustion engine |
DE102009010728C5 (de) * | 2009-02-26 | 2019-08-14 | Federal-Mogul Burscheid Gmbh | Kolbenringe und Zylinderlaufbuchsen |
RU2674177C2 (ru) * | 2013-09-09 | 2018-12-05 | Ниссан Мотор Ко., Лтд. | Высокотеплопроводное поршневое кольцо для двигателя внутреннего сгорания |
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2021
- 2021-04-12 JP JP2021067235A patent/JP7297808B2/ja active Active
- 2021-12-27 KR KR1020237026521A patent/KR20230128362A/ko unknown
- 2021-12-27 MX MX2023009157A patent/MX2023009157A/es unknown
- 2021-12-27 US US18/274,763 patent/US20240026972A1/en active Pending
- 2021-12-27 EP EP21937047.5A patent/EP4276203A1/en active Pending
- 2021-12-27 CN CN202180094895.8A patent/CN116897212A/zh active Pending
- 2021-12-27 WO PCT/JP2021/048637 patent/WO2022219854A1/ja active Application Filing
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2022
- 2022-01-04 TW TW111100233A patent/TWI800200B/zh active
Patent Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US5944920A (en) * | 1996-04-10 | 1999-08-31 | Hitachi Metals, Ltd. | Piston ring material excellent in workability |
JP2008050649A (ja) | 2006-08-24 | 2008-03-06 | Tokusen Kogyo Co Ltd | ピストンリング及びその製造方法 |
JP2010054039A (ja) * | 2008-08-29 | 2010-03-11 | Nippon Piston Ring Co Ltd | 内燃機関用オイルリング |
JP2015108417A (ja) * | 2013-12-05 | 2015-06-11 | 株式会社リケン | 大型ピストンリング及びその素材並びにそれらの製造方法。 |
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Publication number | Publication date |
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EP4276203A1 (en) | 2023-11-15 |
CN116897212A (zh) | 2023-10-17 |
TWI800200B (zh) | 2023-04-21 |
JP7297808B2 (ja) | 2023-06-26 |
MX2023009157A (es) | 2023-08-17 |
US20240026972A1 (en) | 2024-01-25 |
JP2022162404A (ja) | 2022-10-24 |
KR20230128362A (ko) | 2023-09-04 |
TW202239989A (zh) | 2022-10-16 |
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