EP2216423B1 - Steel for fracture split connecting rods - Google Patents

Steel for fracture split connecting rods Download PDF

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Publication number
EP2216423B1
EP2216423B1 EP08858217.6A EP08858217A EP2216423B1 EP 2216423 B1 EP2216423 B1 EP 2216423B1 EP 08858217 A EP08858217 A EP 08858217A EP 2216423 B1 EP2216423 B1 EP 2216423B1
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content
steel
fracture splitting
fracture
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German (de)
English (en)
French (fr)
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EP2216423A1 (en
EP2216423A4 (en
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Akihiro Matsugasako
Goro Anan
Keita Shiihashi
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Kobe Steel Ltd
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Kobe Steel Ltd
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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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • 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
    • C22C38/04—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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese

Definitions

  • the present invention relates to a steel favorably used for producing a connecting rod (hereunder abbreviated as a con'rod occasionally) used as a component in an automobile engine or the like.
  • a connecting rod hereunder abbreviated as a con'rod occasionally
  • An internal-combustion engine such as a gasoline engine or a diesel engine uses a con'rod as a component for connecting a piston to a crankshaft, transferring the reciprocating motion of the piston to the crankshaft, and converting the reciprocating motion to the rotary motion of the crankshaft.
  • the con'rod is a component having a nearly-round through-hole to attach itself to a crankshaft and is configured so that the through-hole portion may be separated (divided) into two nearly-semicircular components in order to facilitate assembly and detachment at maintenance.
  • the portion directly connected to a piston is called a con'rod main body and the other portion is called a con'rod cap.
  • Such a con'rod can be produced, for example, by hot-forging a con'rod main body and a con'rod cap individually and thereafter applying cutting to the mating faces.
  • knock pin processing may be applied in some cases in order to avoid deviation if need arises. If such processing is applied however, arising problems are that the yield quantity of the material deteriorates and the cost increases because many processes are required.
  • a method of assembling a con'rod and a crankshaft by: hot-forging the con'rod integrally; applying machining (through-hole forming (drilling), bolt hole forming, and the like for attaching the con'rod to the crankshaft); thereafter applying fracture splitting process to the con'rod in the cold so that the through-hole portion may be divided into two nearly-semicircular components; and finally interposing the crankshaft, fitting the fracture surfaces, and fastening them with bolts.
  • machinability and fracture splitting performance are hardly compatible.
  • a possible measure to improve machinability is to reduce the content of alloys and lower the hardness of a steel but, if the content of alloys is reduced, the ductility of the steel rises and the fracture splitting performance deteriorates. They are in the relationship of trade-off and are hardly compatible.
  • Patent Document 1 proposes to advance brittle fracture by controlling the contents of Si, V, P, N, Al, Ti, Nb, N, B, and others
  • Patent Document 2 proposes to advance brittle fracture by controlling the contents of Si, V, P, and others
  • Patent Document 3 proposes to advance brittle fracture by controlling the contents of Al, N, and others.
  • Further Patent Documents 1 to 3 describe that brittle fracture can be advanced by adding Ti.
  • a steel for a con'rod however is poor in machinability.
  • a C content is more than 0.5% and alloy elements such as V and Cr are used excessively.
  • JP 2008 208397 A discloses a steel having superior fracture-splittability and machinability for a fracture-splitting type connecting rod.
  • JP 2000 073141 A discloses a hot-refining steel for hot forging and being excellent in breaking splittability.
  • EP 2 000 553 A1 discloses a rolled material for a fracture split connecting rod having excellent fracture splitting characteristics, a hot forged part for a fracture split connecting rod having excellent fracture splitting characteristics and a fracture split connecting rod.
  • the present invention has been established in view of the above circumstances and an object thereof is to provide a steel for a fracture splitting type con'rod that allows fracture splitting performance and machinability to be compatible.
  • the present inventors have found that, when a Ti content is coordinated from the viewpoint of effective Ti (Ti not forming nitride), fracture splitting performance is enhanced rapidly by a very small amount of effective Ti and the effect is saturated immediately thereafter, in contrast machinability lowers gently and the machinability scarcely lowers when an effective Ti content (an f-value) is very small (refer to Fig. 2 ), and consequently both the fracture splitting performance and the machinability can be compatible by controlling a Ti content from the viewpoint of an effective Ti content (an f-value) (refer to Fig. 1 ); and have completed the present invention.
  • a steel for a fracture splitting type connecting rod is characterized in that : the steel contains C: 0.25 - 0.5% (in mass %, the same is applied hereunder), Si: 0.01 - 2.0%, Mn: 0.50 - 2.0%, P: 0.015 - 0.080%, S: 0.01 - 0.2%, V: 0.02 - 0.20%, Cr: 0.05 - 1.0%, Ti: 0.01 - 0.10%, and N: 0.01% or less, with the remainder consisting of iron and inevitable impurities; an f-value represented by the expression (1) shown below is in the range of 0.003 to 0.04; and, in a longitudinal section at a position of D/4 (D is the thickness or the diameter of the steel) from the steel surface, the number of sulfide system inclusions 1 ⁇ m or more in width is 100 to 4,000 pieces per 1 mm 2 , and the average aspect ratio (length/width) of the sulfide system inclusions 1 ⁇ m or more in
  • the steel may further contain one or more kinds of Zr: 0.15% or less, Ca: 0.005% or less, Mg: 0.005% or less, Te: 0.1% or less, REM: 0.3% or less, Al: 0.05% or less, Nb: 0.05% or less, Cu: 1.0% or less, Ni: 1.0% or less, Mo: 1.0% or less, and Bi: 0.1% or less.
  • Zr 0.15% or less
  • Ca 0.005% or less
  • Mg 0.005% or less
  • Te 0.1% or less
  • REM 0.3% or less
  • Al 0.05% or less
  • Nb 0.05% or less
  • Cu 1.0% or less
  • Mo 1.0% or less
  • Bi 0.1% or less
  • a steel according to the present invention preferably, (a) Ti is 0.08% or less and (b) V is 0.10% or less.
  • C is an element necessary for securing strength and enhancing fracture splitting performance. Consequently, the lower limit of a C content is set at 0.25%.
  • a C content is preferably 0.30% or more and yet preferably 0.35% or more. If a C content is excessive however, machinability deteriorates. Consequently, a C content is set at 0.5% or less.
  • a C content is preferably 0.48% or less and yet preferably 0.45% or less.
  • Si is useful as a deoxidizing element when steel is melted and refined.
  • a Si content required for sufficiently exhibiting the effect is preferably 0.01% or more, yet preferably 0.05% or more, and still yet preferably 0.10% or more. If a Si content is excessive however, machinability and hot workability deteriorate. Consequently, a Si content is set at 2.0% or lower.
  • a Si content is preferably 1% or less and yet preferably 0.7% or less.
  • Mn is an element that functions as a deoxidizing and desulfurizing element during melting and refining and prevents cracking during casting. Further, Mn forms sulfide system inclusions (for example, MnS) by combining with S, exhibits notch effect during fracture splitting, and improves fracture splitting performance.
  • a Mn content is set at 0.50% or more.
  • a Mn content is preferably 0.70% or more and yet preferably 0.90% or more. If a Mn content is excessive however, bainite is generated in a metallographic structure and machinability and fracture splitting performance deteriorate. Consequently, a Mn content is set at 2.0% or less.
  • a Mn content is preferably 1.8% or less and yet preferably 1.5% or less.
  • P is an element effective in improving fracture splitting performance since P segregates at grain boundaries and lowers toughness and ductility. Consequently, in order to sufficiently exhibit the effects, a P content is set at 0.015% or more.
  • a P content is preferably 0.020% or more and yet preferably 0.030% or more. If a P content is excessive however, the hot workability of a steel deteriorates. Consequently, a P content is set at 0.080% or less.
  • a P content is preferably 0.070% or less and yet preferably 0.060% or less.
  • S is an element that forms sulfide system inclusions (for example, MnS), improves fracture splitting performance by exhibiting notch effect during fracture splitting, and improves machinability.
  • a S content is set at 0.01% or more.
  • a S content is preferably 0.020% or more and yet preferably 0.030% or more. If a S content is excessive however, hot workability deteriorates. Consequently, a S content is set at 0.2% or less.
  • a S content is preferably 0.1% or less and yet preferably 0.07% or less.
  • V is an element effective in securing the strength of a steel and improving the fracture splitting performance.
  • a V content required for sufficiently exhibiting the effects is preferably 0.02% or more and yet preferably 0.05% or more. If a V content is excessive however, the effects are saturated and the excessive addition causes machinability to deteriorate and the cost to increase. Consequently, a V content is set at 0.20% or less.
  • a V content is preferably 0.19% or less and yet preferably 0.17% or less.
  • a best V content is 0.10% or less. Even if a V content is 0.10% or less, sufficient fracture splitting performance can be secured and, by not adding V excessively, it is possible to secure sufficient machinability even when a machinability improvement element such as Ca that prevents machinability from deteriorating is not added.
  • a V content is preferably 0.08% or less and yet preferably 0.06% or less.
  • Cr is an element contributing to the improvement of strength such as yield strength and fatigue strength.
  • a Cr content required for sufficiently exhibiting the effect is preferably 0.05% or more, yet preferably 0.10% or more, and still yet preferably 0.13% or more. If a Cr content is excessive however, the machinability of a steel deteriorates. Consequently, a Cr content is set at 1.0% or less.
  • a Cr content is preferably 0.90% or less and yet preferably 0.70% or less.
  • Ti is an element important for improving the fracture splitting performance of a steel.
  • a Ti content is set at 0.01% or more.
  • a Ti content is preferably 0.018% or more and yet preferably 0.020% or more. If a Ti content is increased however, the machinability of a steel deteriorates.
  • an effective Ti content an f-value
  • the fracture splitting performance improves rapidly and then the fracture splitting performance does not improve any more even when Ti is added further. Consequently, it is desirable to reduce a Ti content to the utmost limit as long as an after-mentioned effective Ti content (an f-value) is secured.
  • a Ti content is set at 0.10% or less.
  • a Ti content is preferably 0.08% or less, yet preferably 0.07% or less, and still yet preferably 0.06% or less.
  • a Ti content is reduced in order to improve machinability, it is attempted to effectively improve also fracture splitting performance by making use of a small amount of Ti.
  • a N content is set at 0.01% or less.
  • a N content is preferably 0.009% or less and yet preferably 0.007% or less.
  • the lower limit of a N content is not particularly limited but a N content may be 0.002% or more.
  • a steel for a con'rod according to the present invention The basic components of a steel for a con'rod according to the present invention are as described above and the remainder substantially consists of iron. However, it should be acceptable that the steel includes impurities brought in inevitably due to the situation of raw materials, other materials, and production facilities. Further, a steel for a con'rod according to the present invention may arbitrarily contain following elements if needed.
  • Zr, Ca, Mg, Te and REM are elements useful for spheroidizing sulfide system inclusions (for example, MnS) and thus enhancing fracture splitting performance and may be contained in a steel when needed. Since the increase of Mn tends to cause the fracture splitting performance to deteriorate in particular, it is recommended to add Zr, Ca, Mg, Te or REM in order to avoid the influence to the utmost.
  • a Zr content is preferably 0.01% or more and yet preferably 0.05% or more
  • a Ca content is preferably 0.0001% or more and yet preferably 0.001% or more
  • a Mg content is preferably 0.0001% or more and yet preferably 0.001% or more
  • a Te content is preferably 0.0001% or more and yet preferably 0.001% or more
  • a REM content is preferably 0.0001% or more and yet preferably 0.001% or more.
  • a Zr content is preferably 0.13% or less (yet preferably 0.12% or less), a Ca content is preferably 0.004% or less (yet preferably 0.003% or less), a Mg content is preferably 0.004% or less (yet preferably 0.003% or less), a Te content is preferably 0.05% or less (yet preferably 0.03% or less), and a REM content is preferably 0.1% or less (yet preferably 0.05% or less).
  • Zr, Ca, Mg, Te and REM may be added individually or in combination.
  • Al and Nb are elements useful for deoxidizing and crystal grain refining and contribute to the enhancement of strength.
  • an Al content is preferably more than 0.01% and yet preferably 0.02% or more, and a Nb content is preferably 0.01% or more and yet preferably 0.02% or more. If those elements are added excessively however, the effects are saturated and hence the upper limits are set as stated above.
  • An Al content is preferably 0.04% or less (yet preferably 0.035% or less) and an Nb content is preferably 0.045% or less
  • Ca may be added to a steel in some cases as stated above.
  • a nozzle is likely to clog.
  • Cu, Ni, and Mo are elements contributing to the improvement of the strength of a steel and may be contained in the steel if needed.
  • a Cu content is preferably 0.01% or more and yet preferably 0.05% or more
  • a Ni content is preferably 0.01% or more and yet preferably 0.1% or more
  • a Mo content is preferably 0.01% or more and yet preferably 0.1% or more. If a Cu content is excessive however, marks are generated on a steel surface during production. Meanwhile, if a Ni content is excessive, the effect is saturated and the excessive addition causes the cost to increase. Moreover, if a Mo content is excessive, the machinability of a steel deteriorates. Consequently, when those elements are contained, the upper limits are set as stated above.
  • a Cu content is preferably 0.5% or less
  • a Ni content is preferably 0.5% or less
  • a Mo content is preferably 0.7% or less.
  • Bi is an element contributing to the improvement of machinability.
  • a Bi content required for sufficiently exhibiting the effect is preferably 0.001% or more and yet preferably 0.01% or more. The effect is saturated if a Bi content is excessive however, and hence the upper limit is set as stated above.
  • a Bi content is preferably 0.08% or less.
  • a feature of the present invention lies in the fact that an effective Ti content (an f-value) is appropriately controlled while steel components are drawn up in the aforementioned ranges.
  • An effective Ti content means a content of Ti obtained by subtracting a content of TiN from a content of Ti in a steel and is referred to as an f-value occasionally in the present description.
  • fracture splitting performance is coordinated from the viewpoint of an effective Ti content, the fracture splitting performance advances rapidly by a very small amount of effective Ti and the effect is saturated immediately thereafter.
  • machinability lowers gently and the machinability scarcely lowers when an effective Ti content (an f-value) is very small. Consequently, both the fracture splitting performance and the machinability can be improved by using Ti of a quantity enough to secure an effective Ti content (an f-value) necessary for rapidly increasing the fracture splitting performance in the requisite minimum.
  • An effective Ti content (an f-value) is given by the following expression (1).
  • An effective Ti content (an f-value) required for surely securing fracture splitting performance is 0.003 or more, preferably 0.005 or more, and yet preferably 0.008 or more. If an effective Ti content (an f-value) increases however, the quantity of added Ti increases and machinability is likely to deteriorate. Consequently, an effective Ti content (an f-value) is preferably 0.04 or less, yet preferably 0.02 or less, and still yet preferably 0.015 or less.
  • f Ti - N ⁇ x ⁇ 48 / 14 (in the expression, [Ti] and [N] represent the contents (mass %) of Ti and N in a steel, respectively)
  • fracture splitting performance is secured by surely satisfying the aforementioned lower limit of an effective Ti content (an f-value) and, on top of that, the upper limit of the effective Ti content (the f-value) and the upper limit of the Ti content in a steel are reduced to the utmost.
  • an effective Ti content (an f-value) and a Ti content in a steel are reduced to the utmost, the effective Ti content (the f-value) is 0.015 or less and the Ti content is 0.06% or less in a steel.
  • sulfide system inclusions for example, MnS.
  • the sulfide system inclusions are elongated by rolling and hot forging in the directions of the rolling and the forging.
  • the elongated sulfide system inclusions exist in the longitudinal direction (elongated in the direction perpendicular to a fracture splitting face) at the time of the fracture splitting of a steel, the sulfide system inclusions peel off from a metal matrix and stress relaxation occurs in accordance with the progression of cracks.
  • brittle fracture is hindered, toughness and ductility are enhanced, and fracture splitting performance is caused to deteriorate.
  • the size and the shape of sulfide system inclusions necessary for exhibiting the fracture splitting performance improving effect are quantitatively represented as follows. That is, in a steel according to the present invention, in a longitudinal section at a position of D/4 (D is the thickness or the diameter of the steel) from the steel surface, the number of sulfide system inclusions 1 ⁇ m or more in width is 100 or more pieces per 1 mm 2 , and the arithmetic average of the aspect ratios (length/width) (the average aspect ratio) of the sulfide system inclusions 1 ⁇ m or more in width is 15 or less.
  • An average aspect ratio is preferably 10 or less, yet preferably 8 or less, and still yet preferably 6 or less. It is desirable that an average aspect ratio is as close to one as possible.
  • the lower limit of an average aspect ratio is not particularly limited but an average aspect ratio may be 2 or more (or 3 or more).
  • the number of sulfide system inclusions 1 ⁇ m or more in width is preferably 300 or more pieces and yet preferably 400 or more pieces per 1 mm 2 . If the number of sulfide system inclusions increases however, defects such as cracks tend to be generated during rolling and hot forging. Consequently, the number of sulfide system inclusions 1 ⁇ m or more in width is set at 4,000 or less pieces per 1 mm 2 . It is recommended to control the number of sulfide system inclusions 1 ⁇ m or more in width to preferably 3,000 or less pieces and yet preferably 2,500 or less pieces per 1 mm 2 .
  • sulfide system inclusions mainly means MnS in the present invention but includes other sulfide and complex sulfide.
  • the width, the average aspect ratio (length/width), and the number of pieces of sulfide system inclusions are the values obtained by observing a visual field of 1 mm 2 with an optical microscope at a magnification of 1,000 in a longitudinal section at a position of D/4 (D is the thickness or the diameter of a steel) from a steel surface.
  • the size and the shape of sulfide system inclusions can be controlled in prescribed ranges by appropriately setting rolling conditions in proportion to the contents of Mn, S, and added inclusion spheroidizing elements (Zr, Ca, Mg, Te, REM, and other elements).
  • rolling conditions it is recommended to select the rolling start temperature from the range of 1,000°C or higher and the rolling end temperature from the range of 850°C or higher.
  • the aspect ratio of sulfide system inclusions is likely to reduce and a prescribed value is likely to be satisfied.
  • sulfide system inclusions are likely to precipitate by using Ti precipitates such as TiC and TiN as nuclei, the sulfide system inclusions having small aspect ratios precipitate in large numbers when a steel contains Ti.
  • a visual field of 1 mm 2 is observed with an optical microscope (1,000 magnifications) and the number of sulfide system inclusions 1 ⁇ m or more in width is counted. Further, the aspect ratios of the sulfide system inclusions 1 ⁇ m or more in width are measured and the arithmetic average is obtained.
  • Each of the bar steels obtained in the test example is cut into an appropriate length, heated to a temperature of 1,200°C, flattened to a thickness of 25 mm by forging, and thereafter air-cooled.
  • the obtained flat plate is cut and a test piece shown in Fig. 3 is obtained.
  • Fig. 3(a) shows the top view of a test piece
  • Fig. 3(b) shows the side view of a test piece
  • the symbol a represents notches
  • the symbol b represents bolt holes
  • the symbol c is the arrow showing the rolling direction
  • the test piece has a tabular shape of 65 mm x 65 mm x 22 mm in thickness and a cylindrical hole 43 mm in diameter is bored in the center.
  • bolt holes b (8.3 mm in diameter) are formed in the test piece in the rolling direction.
  • holders 3a and 3b are inserted into the center hole of a test piece 6, they are set in a press test apparatus (1,600 t press), fracture splitting is applied to the test piece 6 at a press speed of 270 mm/s.
  • the fracture speed of the test piece is about 150 mm/s by calculation because the wedge angle of wedges 4 and 5 is 30°.
  • the difference of the hole diameter (L2 - L1) between before and after the fracture splitting is measured as the dimension change and the case where the dimension change is 0.15 mm or less is evaluated as being excellent in fracture splitting performance.
  • the criterion of 0.15 mm or less dimension change is identical to the criterion stipulated in C70S6 of the DIN standards used in Europe.
  • Milling is applied to the cut plane of a bar steel obtained in the test example, thereafter drilling is applied to the milling plane under the following conditions, and the distance (the total length) of the drilling until a tool breaks or is damaged by melting is measured;
  • Cutting tool SKH51 ( ⁇ 10 straight drill), Cutting speed: 30 m/min, Feed: 0.15 mm/rev., Drilling depth: 30 mm, Lubrication state: Dry, and Drilling position: D/4 (D is the diameter of a bar steel).
  • Tool service life is evaluated by a relative value obtained from the drilling distance L of each bar steel by using the drilling distance L A1 of the steel type A1 in Table 1 as the standard.
  • Tool service life L / L A ⁇ 1
  • Test example 2 is carried out in the same way as Test example 1 except that steels of the chemical compositions shown in Tables 2 and 3 are used in Test example 2.
  • the tool service life in each of the groups B to H and J is shown by a relative value obtained by rating the tool service life of the steel type to which Ti is not added as 1.
  • Test example 3 is carried out in the same way as Test example 1 except that the steel type H2 shown in Table 2 is used and the rolling start temperature and the rolling end temperature are set as shown in Table 8 below in Test example 3.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Shafts, Cranks, Connecting Bars, And Related Bearings (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
EP08858217.6A 2007-12-03 2008-11-28 Steel for fracture split connecting rods Not-in-force EP2216423B1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2007312523 2007-12-03
PCT/JP2008/071702 WO2009072445A1 (ja) 2007-12-03 2008-11-28 破断分割型コネクティングロッド用鋼

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EP2216423A1 EP2216423A1 (en) 2010-08-11
EP2216423A4 EP2216423A4 (en) 2014-12-10
EP2216423B1 true EP2216423B1 (en) 2015-09-30

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US (1) US20100266439A1 (pt)
EP (1) EP2216423B1 (pt)
JP (1) JP4264460B1 (pt)
KR (1) KR20100070386A (pt)
CN (1) CN101883873B (pt)
BR (1) BRPI0819104A2 (pt)
WO (1) WO2009072445A1 (pt)

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JP5432590B2 (ja) * 2009-05-20 2014-03-05 株式会社神戸製鋼所 破断分割性に優れた熱間鍛造部品とその製造方法、および自動車用内燃機関部品
WO2012157455A1 (ja) 2011-05-19 2012-11-22 住友金属工業株式会社 非調質鋼および非調質鋼部材
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
JP5778055B2 (ja) 2012-02-15 2015-09-16 新日鐵住金株式会社 熱間鍛造用圧延棒鋼および熱間鍛造素形材ならびにコモンレールおよびその製造方法
WO2016143812A1 (ja) * 2015-03-09 2016-09-15 新日鐵住金株式会社 熱間圧延鋼材および鋼部品
WO2017069161A1 (ja) * 2015-10-19 2017-04-27 新日鐵住金株式会社 熱間圧延鋼材および鋼部品
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US20100266439A1 (en) 2010-10-21
CN101883873B (zh) 2012-10-31
EP2216423A1 (en) 2010-08-11
CN101883873A (zh) 2010-11-10
EP2216423A4 (en) 2014-12-10
KR20100070386A (ko) 2010-06-25
WO2009072445A1 (ja) 2009-06-11
JP2009155724A (ja) 2009-07-16

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