WO2004083475A1 - 非調質コネクティングロッド及びその製造方法 - Google Patents
非調質コネクティングロッド及びその製造方法 Download PDFInfo
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- WO2004083475A1 WO2004083475A1 PCT/JP2004/003439 JP2004003439W WO2004083475A1 WO 2004083475 A1 WO2004083475 A1 WO 2004083475A1 JP 2004003439 W JP2004003439 W JP 2004003439W WO 2004083475 A1 WO2004083475 A1 WO 2004083475A1
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- Prior art keywords
- ferrite
- hardness
- connecting rod
- large end
- steel
- Prior art date
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Classifications
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
- F16C7/00—Connecting-rods or like links pivoted at both ends; Construction of connecting-rod heads
- F16C7/02—Constructions of connecting-rods with constant length
- F16C7/023—Constructions of connecting-rods with constant length for piston engines, pumps or the like
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
- F16C9/00—Bearings for crankshafts or connecting-rods; Attachment of connecting-rods
- F16C9/04—Connecting-rod bearings; Attachments thereof
- F16C9/045—Connecting-rod bearings; Attachments thereof the bearing cap of the connecting rod being split by fracturing
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T29/00—Metal working
- Y10T29/49—Method of mechanical manufacture
- Y10T29/49229—Prime mover or fluid pump making
- Y10T29/49288—Connecting rod making
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T29/00—Metal working
- Y10T29/49—Method of mechanical manufacture
- Y10T29/49229—Prime mover or fluid pump making
- Y10T29/49288—Connecting rod making
- Y10T29/49291—Connecting rod making including metal forging or die shaping
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T74/00—Machine element or mechanism
- Y10T74/21—Elements
- Y10T74/2142—Pitmans and connecting rods
Definitions
- the present invention relates to a non-heat-treated connecting rod and a method for producing the same, and more particularly, to a non-heat-treated connecting rod excellent in machinability, fracture splitting property and fatigue resistance suitable for a connecting rod for an automobile engine or the like. It relates to a connecting rod and its manufacturing method. Background art
- the connecting rod 1 shown in Fig. 1 which is a component of an automobile engine and the like, is manufactured by hot-forging the connecting rod body 2 and the connecting rod cap 3 in separate processes and then quenching and tempering them. This was followed by a refining treatment, followed by machining of the bolt holes by machining and finish shaping, and then by bolts 4 to connect to a complex crankshaft and assembled.
- both the connecting rod body 2 and the connecting port cap 3 have been integrally formed by hot forging.
- a so-called “cracking connecting rod” that is divided at the end 5 into a connecting port main body 2 and a connecting rod cap 3 (hereinafter also referred to as “cracking”) is being studied.
- a method is used in which a jig is inserted into the hole at the large end 5 (for example, the N section in Fig. 1), which is the part of the integrally formed material to be divided, and the jig is broken by applying stress.
- the cracked connecting rod 1 (that is, the cracking connecting rod) is used to connect the connecting rod body 2 to the crankshaft if it has a smooth brittle fracture surface. After sandwiching the crankshaft with the connecting rod cap 3 and the fracture surface, the connecting rod body 2 and the connecting rod cap 3 need only be connected with the port 4. Therefore, if the cracking connecting rod has a smooth brittle fracture surface, it is not necessary to cut the mating surface that sandwiches the crankshaft, and the manufacturing cost can be reduced. Since the connection is made at the fractured surface, the effect of excellent fastening rigidity, that is, excellent strength can be obtained.
- the cracking connecting rod is made of a non-heat treated steel containing about 0.7% by mass of C (carbon) as disclosed in US Pat. No. 5,135,887. Has already been commercialized in Europe. Only however, the above non-tempering-connecting rods put into practical use in Europe have a high C content and are inferior in machinability to conventional connecting rods that have been tempered with carbon steel for machine structural use. For this reason, it has not always been possible to meet the demands of the industry to improve machinability for boring holes. Furthermore, the fatigue limit of non-heat treated connecting rods practically used in Europe (hereinafter, the fatigue limit is referred to as fatigue strength and is indicated by aw) is the value of the connecting rod prepared by tempering carbon steel for machine structural use. 0.35% C-0.4% S i-0.95% M n-0.04% S-0.5% C r-0.1 It is inferior to the fatigue strength of non-heat treated connecting rods with a basic chemical composition of% V.
- Japanese Patent Application Laid-Open No. H11_3154340 discloses that in a low carbon region having a C content of 0.2 to less than 0.35% by weight, the Mn content is reduced and the V content is increased.
- the steel for machine structural use proposed in this patent publication merely contains S in an amount of 0.01 to 0.2% by weight in order to improve machinability. It is not always possible to satisfy the machinability required for connecting rods
- the present invention has been made in view of the above-mentioned circumstances, and an object of the present invention is to provide a Pb-free steel excellent in machinability, cracking properties, and fatigue resistance suitable for a connecting rod of an automobile engine or the like. An object of the present invention is to provide a non-heat treated connecting rod as a material and a method for producing the same.
- the gist of the present invention resides in the following (I) non-tempering connecting rod and ( ⁇ ) non-tempering connecting rod manufacturing method.
- the symbol of the element in the formula (1) represents the content of the element in steel in mass%.
- the total hardness of ferrite perlite is 255 to 320 in terms of Vickers hardness, and the hardness of ferrite in the ferrite perlite structure at the large end is 2 in Vickers hardness.
- the symbol of the element in the formula (1) represents the content of the element in steel in mass%.
- invention relating to the non-heat treated connecting rod of the above (I) and the invention relating to the method for producing the non heat treated connecting rod of the above ( ⁇ ) are referred to as invention (I) and invention ( ⁇ ), respectively. . These may be collectively referred to as the present invention.
- the ferrite-perlite structure in the present invention refers to a mixed structure of ferrite and perlite. Each of the above phases can be confirmed by observation using an optical microscope or an electron microscope.
- the total hardness of the large end refers to the average value of four randomly measured planes cut perpendicular to the forging axis, and the Vickers hardness as the total hardness of the large end is 98.0 A value measured at a test force of 7 N.
- Vickers hardness as the hardness of ferrite is a value measured with a test force of 0.0987 N.
- the ferrite referred to in the present invention does not include ferrite that forms perlite together with cementite.
- Figure 1 is a diagram showing the details of the connecting rod.
- FIG. 2 is a view for explaining a dimension measurement point for deriving a breaking strain amount.
- the present inventors conducted various studies in order to achieve the above-mentioned object, and
- the steel structure is a ferrite-perlite structure.
- the present invention has been completed based on the above findings.
- C has an effect of increasing the strength of steel, and an effect can be obtained by containing 0.25% or more.
- the content exceeds 0.35%, the hardness increases but the ferrite ratio decreases, and the durability ratio, that is, the fatigue strength Degree (aw) // Tensile strength (TS) "becomes smaller, so the fatigue strength does not increase when the hardness increases, and conversely, the machinability decreases because the hardness increases. Therefore, the content of C is set to 0.25 to 0.35%.
- Si is effective in deoxidizing steel and has the effect of increasing the strength of steel by solid solution strengthening. A sufficient effect can be obtained by containing 0.5% or more. However, if the content of Si exceeds 0.70%, the hot workability of the steel decreases, causing defects such as cracks during forging, and an excessive load on the forging die. Therefore, the content of 31 was set to 0.50 to 0.70%.
- Mn not only has a deoxidizing effect on steel, but also has an effect of improving hardenability and improving the strength of steel.
- the content of Mn needs to be 0.60% or more.
- the content of Vln exceeds 0.90%, the hot workability of the steel decreases, and bainite is easily formed, and the fatigue strength, cracking properties and machinability decrease. There is.
- the cost of ingredients rises. Therefore, the content of Mn was set to 0.60 to 0.90%.
- the P segregates at the crystal grain boundaries to embrittle the steel, and has the effect of making the fracture surface during cracking of the connecting rod a smooth brittle fracture surface.
- the P content needs to be 0.040% or more. However, if its content exceeds 0.070%, the hot workability of the steel may decrease. Therefore, the content of P is set to be 0.040 to 0.070%.
- the content of S forms a sulfide together with Mn and Ti to enhance the machinability of steel.
- the content of S should be 0.040% or more. There is a need. However, if the S content exceeds 0.130%, the hot workability of the steel may decrease. Therefore, the content of S is set to 0.040 to 0.130%. It is preferable that the content of S exceeds 0.070% to 0.130 ° / 0 .
- the content of 1: 1: must be 0.10% or more. However, if the content exceeds 0.20%, bainite is likely to be generated, and the component cost also increases. Therefore, the Cr content was set to 0.10 to 0.20%.
- V is an important element in the present invention. That is, V has a function of improving the strength by being precipitated as a carbonitride in ferrite, and has an effect of increasing cracking properties by being added in combination with Ti described later. To obtain these effects sufficiently, the V content needs to be 0.15% or more. However, when the content exceeds 0.20%, the component cost increases. Therefore, the content of V is set to 0.15 to 0.20%.
- T i is an important element in the present invention. That is, as in the case of D, the carbon is precipitated as carbonitride in the ferrite to increase the strength, and further has the effect of significantly strengthening the ferrite by being added in combination with V. This strengthening of ferrite reduces the difference between the total hardness in ferrite's perlite structure and the hardness of ferrite, so that good cracking performance can be ensured.Ferrite strengthening can also ensure great fatigue strength. Connect. T i also has the effect of forming sulfides and improving machinability. In order to obtain the above-mentioned effects sufficiently, it is necessary to contain 0.15% or more of Ding1. It is necessary. However, if the content exceeds 0.20%, the component cost increases. Therefore, the content of Ding 1 was set to 0.15 to 0.20%.
- N forms carbonitrides with V and Ti and contributes to strengthening of the steel.
- the content of N is required to be 0.002% or more.
- the content of N was set to 0.002 to 0.020%.
- the large-end structure of the non-heat treated connecting rod according to the present invention needs to be ferrite perlite. This is to improve both cracking and machinability, facilitate cracking at the large end, and facilitate machining of bolt holes.
- the organization containing martensite, venaite / austenite has low cracking ability, Poor machinability compared to ferrite and perlite structures. Therefore, in the non-heat treated connecting rod according to the present invention, the structure at the large end is made of ferrite perlite.
- ferrite 'perlite organization refers to a mixed organization of ferrite and perlite.
- the large end of the non-heat treated connecting rod according to the present invention has a Vickers hardness of 255 to 320 in total hardness and a Vickers hardness of ferrite in the perlite structure.
- the ratio between the hardness of the ferrite and the total hardness must be at least 0.80.
- the fatigue strength and cracking properties decrease, while if it exceeds 320, large fatigue strength and good cracking properties are obtained. Although it can be secured, machinability may decrease.
- the hardness of the ferrite in the ferrite-peralite structure affects the cracking properties, machinability and fatigue strength, and it is preferable that the hardness of the ferrite be Hv250 or higher for good cracking properties. This is a condition for ensuring machinability and large fatigue strength.
- the total hardness is 255 to 320 in terms of Vickers hardness, and the hardness of ferrite in the ferrite perillat structure. With a Vickers hardness of at least 250, and The ratio between the hardness of the ferrite and the total hardness was set to 0.80 or more.
- the total hardness of the large end refers to the average value of four randomly measured surfaces cut perpendicular to the forging axis
- the Vickers hardness as the total hardness of the large end is The value measured at a test force of 0.908 N, the Vickers hardness of the ferrite, is a value measured at a test force of 0.0987 N. It is as stated.
- the ferrite referred to in the present invention does not include ferrite that forms perlite together with cementite.
- the invention (I) is a non-refined connecting rod that satisfies the provisions of the above (A) and (B).
- the invention ( ⁇ ) is to produce a steel having the chemical composition described in the above (A) into a steel ingot and a steel slab after being melted by a normal method, and then to leave the steel ingot or steel slab as it is. Or after further performing hot rolling and Z or forging by a usual method, in a step including the above-mentioned processes (a) to (e) in this order, the connecting port main body and the connecting port are formed. It is divided into a cap and then, after the process (f), it is connected to the crankshaft and assembled.
- the process (a) is a heating process for hot forging as an integrated body in which the connecting rod body and the connecting rod cap are connected. If the heating temperature for forging is lower than 1200 ° C., the solid solution of T i in the base material becomes insufficient, and even if T i and V are added in combination, Even with a steel having a chemical composition, significant strengthening of ferrite cannot be achieved, and the desired good cracking properties and large fatigue strength cannot be obtained. Sometimes. On the other hand, if the heating temperature exceeds 135 ° C., an excessive load is imposed on the heating furnace, and the scale loss increases, resulting in an increase in cost. As described above, the heating temperature of the steel having the chemical composition described in the above item (A) is preferably 1200 to 135 ° C.
- the temperature of the heat treatment of (a) was set to 1200 to: 135 ° C.
- the process (b) is hot forging for processing into an integrated body in which the connecting rod body and the connecting rod cap are connected. If the forging temperature is lower than 900 ° C, the deformation resistance of the material (forged material) is large, and the life of the forging die may be shortened. Furthermore, since the austenite crystal grains are not sufficiently recrystallized to undergo ferrite-pearlite transformation and the structure is refined, the toughness is increased, the cracking property is reduced, and the total hardness and ferrite hardness are reduced. In some cases, the fatigue strength is reduced and the cracking performance is reduced. For this reason, it is preferable to perform hot forging at a temperature of 900 ° C or more to process the connecting rod body and the connecting rod cap into an integrated product.
- the hot forging temperature of (b) was set to 900 ° C. or more. Note that this forging is more preferably performed at a temperature of 150 ° C. or more.
- the upper limit temperature of forging if the heating temperature is 120 to 135 ° C., the substantial upper limit temperature is about 125 ° C.
- the process (c) is a hot coining process applied to the large end to satisfy the specified dimensional tolerance.
- Coining of the large end is usually performed cold, but if the large end is coined at a low temperature of 800 ° C or less, the coining occurs when cracking occurs later. Since the residual stress is released, the adhesion to the fracture surface is reduced, and it may be necessary to perform cutting on the mating surface that sandwiches the crankshaft.When cutting is performed, the number of processes increases. The cost will also increase. Because of this, The coining process applied to the large end to satisfy the dimensional tolerance is preferably performed at a temperature exceeding 800 ° C.
- the coining process applied to the large end of (c) is performed at a temperature exceeding 800 ° C.
- the steel having the chemical composition described in the above (A) is subjected to the treatment described in the above (a) to (c), and after the hot coining of (c) is performed, cooling is performed in the air.
- cooling is performed in the air.
- the temperature in the above (a) to (c) refers to the value on the surface of steel or a monolithic molded material.
- the invention ( ⁇ ) does not specify the coining temperature of the part other than the large end, and the coining treatment of the part other than the large end may be performed hot or may be performed as usual. It may be performed cold.
- a notch is provided at the large end in the processing of (d). It is extremely preferable that the notch provided at the large end has a stress concentration coefficient of 2 or more, and the notch provided at the large end is preferably provided at the N portion in FIG.
- the process (e) is a process of dividing the integrally formed material into a connecting rod body and a connecting rod cap.
- the method of this treatment is not particularly limited, and it may be performed by a usual method of manufacturing a cracking connecting rod.
- the connecting mouth main body and the connecting mouth head cap divided by the cracking process are connected to the crankshaft. This is the process of assembling together.
- the method of this treatment is not particularly limited, and may be performed by a usual method of manufacturing a connecting pad.
- the bolt hole processing for connecting the connecting port main body and the connecting rod cap may be performed, for example, before the above-mentioned processing (d), simultaneously with the processing of (d) or before the cracking processing of (e). You can go to
- a steel ingot having the chemical composition shown in Table 1 was smelted by a conventional method using a 3 ton electric furnace to form a steel ingot.
- steels 3 to 5 and steels 10 to 12 are steels according to the present invention whose chemical compositions are within the range specified in the present invention
- steel 1, steel 2 and steels 6 to 9 are components of Any of the steels of Comparative Examples is out of the content range specified in the present invention.
- steel 1 and steel 2 are almost equivalent to the steels for cracking connecting openings disclosed in U.S. Pat.No. 5,135,587 and already in practical use in Europe.
- the steel of the present invention and the steel of the comparative example were formed into billets by a conventional method, and then hot-rolled into round bars having a diameter of 35 mm.
- the connecting rod body and the connecting port cap were integrally formed and forged, and the large end portion was coined.
- Table 2 shows the conditions for the above-described integral forming forging and coining of the large end.
- the cooling after hot coining of the large end was allowed to cool in the air.
- coining was performed in a portion other than the large end portion in a cold state, and a notch having a stress concentration coefficient shown in Table 2 was provided in the N portion in FIG.
- the asterisk indicates that the steel has a chemical composition outside the conditions specified in the present invention.
- Hv hardness Vickers hardness (hereinafter referred to as Hv hardness), tensile properties, fatigue resistance properties, machinability and cracking properties were investigated.
- an optical microscope having a magnifying power of 400 times after cutting out a micro test piece having a surface perpendicular to the forging axis as an observation surface from the large end portion of each of the above-mentioned integrally formed materials, mirror-polished and subjected to nital corrosion.
- the microstructure was determined by observing at.
- the Hv hardness of the ferrite was further measured at a test force of 0.0987N.
- test piece was cut from the large end of each integrally formed material with the surface perpendicular to the forging axis as the test surface, and after mirror polishing, the HV hardness as the total hardness was 98.0.
- the diameter of the parallel part described in JIS Z 2201 was 3.0 mm from the rod part 6 (see Fig. 1) of the connecting rod body 2 of the integrally molded material.
- a 14A tensile test piece was cut out and subjected to a tensile test at room temperature to measure the tensile strength (TS).
- the tissue was ferrite-perlite
- the diameter of the parallel part from the rod part 6 of the connecting rod body 2 of the integrally formed material was 3 mm, and the length of the parallel part was 11 mm.
- a fatigue test piece was cut out from the test piece and subjected to load-controlled tension-compression using an electro-hydraulic servo-servo type fatigue tester at room temperature and air with a stress ratio of _1 and a repetition rate of 10 to 20 Hz.
- a test was performed and the fatigue strength (aw) was measured.
- the durability ratio ( ⁇ w / T S) was determined from this ⁇ w and the aforementioned T S.
- the machinability is determined by assuming the drilling of bolt holes, by drilling through holes in the large end of each integrally formed material and drilling the corners of the drill after drilling 300 holes (that is, Was measured and evaluated.
- Test No. 2 was conducted using steel 2 which is a steel equivalent to the steel for non-heat-treating connecting rods used in some vehicle types and which contains Pb and Ca for the purpose of improving machinability.
- the above-mentioned corner wear amount is used as a reference value, and if the wear amount is within 110% of the above-mentioned reference value, the machinability is “ ⁇ ”, and if it exceeds 110% of the above-mentioned reference value, the machinability is “ X ". This is because it is unlikely that the machinability of steel containing no Pb or Ca is significantly improved as compared with the machinability of steel 2 containing Pb and Ca, and the wear amount is lower than the reference value. It is judged that production on an industrial scale is possible if it is within 110% of the above.
- the piercing test conditions are as follows.
- Drill P20 Carbide straight shank drill with a diameter of 8 mm, number of revolutions: 1200 rpm,
- Lubrication water-soluble lubricant.
- each integrally formed material with a bolt hole machined at the large end was cracked on the connecting rod body and connecting port pad cap by the usual falling weight method. It was not possible to crack the connecting rod body and the connecting rod cap by the falling weight method only with the integrally formed material made of steel 2.
- Step 1 whose fracture surface was equivalent to steel for cracking connecting rods already in practical use in Europe was used as the material.
- the cracking property was determined to be good when the fracture surface was about the same as that when the steel sheet 1 was used and the fracture strain amount was smaller than 0.15 mm, which is the fracture strain amount when the steel 1 was used as a material.
- a to c shown in Fig. 2 This is the value obtained by subtracting the value of "a- ⁇ (b + c) / 2 ⁇ " before cracking from the value of "a- ⁇ (b + c) / 2 ⁇ " after cracking.
- Hv represents the hardness of the ferrite in the Vickers hardness at the large end
- ⁇ represents the total hardness of the large end at the Vickers hardness.
- the asterisk indicates that the conditions are out of the conditions specified in the present invention.
- test number 12 the cracking property was extremely good because the notch with the large stress concentration coefficient was provided.
- Test Nos. 6 to 9 at least one of the machinability, cracking property and fatigue resistance property is required because the chemical composition is out of the conditions specified in the present invention. The goal has not been reached.
- Test No. 10 has the chemical composition specified by the present invention, the hardness of the ferrite in the ferrite / pearlite structure at the large end is out of the conditions specified in the present invention, so that the cracking property and the durability are high. Poor fatigue properties.
- Test No. 11 has the chemical composition specified by the present invention, the total hardness and ferrite hardness are out of the conditions specified by the present invention, and the cracking property and the fatigue resistance are inferior. ing. Industrial applicability
- the non-heat treated connecting rod of the present invention is made of non-Pb-added steel and has excellent machinability, cracking properties and fatigue resistance properties, and can be used as a connecting rod for automobile engines and the like. Can be.
- This non-tempered connecting rod can be manufactured relatively easily by the method of the present invention.
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- Engineering & Computer Science (AREA)
- General Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Shafts, Cranks, Connecting Bars, And Related Bearings (AREA)
- Heat Treatment Of Steel (AREA)
- Forging (AREA)
Abstract
Description
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Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
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EP04720729A EP1605071B1 (en) | 2003-03-18 | 2004-03-15 | Non-quenched/tempered connecting rod and method of producing the same |
DE602004017144T DE602004017144D1 (de) | 2003-03-18 | 2004-03-15 | Nicht abgeschreckte/getemperte pleuelstange und zugehöriges herstellungsverfahren |
US11/221,853 US8152939B2 (en) | 2003-03-18 | 2005-09-09 | Non-heat treated connecting rod and method of manufacturing the same |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
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JP2003072949 | 2003-03-18 | ||
JP2003-072949 | 2003-03-18 |
Related Child Applications (1)
Application Number | Title | Priority Date | Filing Date |
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US11/221,853 Continuation US8152939B2 (en) | 2003-03-18 | 2005-09-09 | Non-heat treated connecting rod and method of manufacturing the same |
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WO2004083475A1 true WO2004083475A1 (ja) | 2004-09-30 |
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PCT/JP2004/003439 WO2004083475A1 (ja) | 2003-03-18 | 2004-03-15 | 非調質コネクティングロッド及びその製造方法 |
Country Status (6)
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US (1) | US8152939B2 (ja) |
EP (1) | EP1605071B1 (ja) |
CN (1) | CN100357472C (ja) |
DE (1) | DE602004017144D1 (ja) |
TW (1) | TWI255859B (ja) |
WO (1) | WO2004083475A1 (ja) |
Cited By (2)
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EP1780296A1 (en) * | 2005-10-26 | 2007-05-02 | Nissan Motor Co., Ltd. | Non-heat treated steel for connecting rod and connecting rod formed of same |
CN105463318A (zh) * | 2015-11-27 | 2016-04-06 | 北大方正集团有限公司 | 非调质钢、其生产方法及利用其制造的涨断连杆 |
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JP5703991B2 (ja) * | 2011-06-24 | 2015-04-22 | スズキ株式会社 | コンロッドの破断分割方法及びその装置 |
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- 2004-03-15 DE DE602004017144T patent/DE602004017144D1/de not_active Expired - Lifetime
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Also Published As
Publication number | Publication date |
---|---|
EP1605071B1 (en) | 2008-10-15 |
TWI255859B (en) | 2006-06-01 |
US8152939B2 (en) | 2012-04-10 |
CN100357472C (zh) | 2007-12-26 |
EP1605071A4 (en) | 2007-08-29 |
TW200426228A (en) | 2004-12-01 |
EP1605071A1 (en) | 2005-12-14 |
DE602004017144D1 (de) | 2008-11-27 |
CN1761769A (zh) | 2006-04-19 |
US20060000088A1 (en) | 2006-01-05 |
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