TWI586814B - Steel wire for mechanical structure parts - Google Patents
Steel wire for mechanical structure parts Download PDFInfo
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- TWI586814B TWI586814B TW105109031A TW105109031A TWI586814B TW I586814 B TWI586814 B TW I586814B TW 105109031 A TW105109031 A TW 105109031A TW 105109031 A TW105109031 A TW 105109031A TW I586814 B TWI586814 B TW I586814B
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- cementite
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- 229910000831 Steel Inorganic materials 0.000 title claims description 76
- 239000010959 steel Substances 0.000 title claims description 76
- 229910001567 cementite Inorganic materials 0.000 claims description 119
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 claims description 119
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 72
- 229910000859 α-Fe Inorganic materials 0.000 claims description 33
- 239000013078 crystal Substances 0.000 claims description 31
- 239000002184 metal Substances 0.000 claims description 27
- 229910052751 metal Inorganic materials 0.000 claims description 27
- 229910052742 iron Inorganic materials 0.000 claims description 24
- 229910052750 molybdenum Inorganic materials 0.000 claims description 7
- 229910052802 copper Inorganic materials 0.000 claims description 6
- 229910052698 phosphorus Inorganic materials 0.000 claims description 5
- 229910052799 carbon Inorganic materials 0.000 claims description 4
- 229910052757 nitrogen Inorganic materials 0.000 claims description 4
- 229910052782 aluminium Inorganic materials 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- 229910052710 silicon Inorganic materials 0.000 claims description 3
- 238000001816 cooling Methods 0.000 description 113
- 238000005097 cold rolling Methods 0.000 description 46
- 238000010438 heat treatment Methods 0.000 description 44
- 238000012360 testing method Methods 0.000 description 32
- 238000000034 method Methods 0.000 description 22
- 239000002436 steel type Substances 0.000 description 22
- 238000004519 manufacturing process Methods 0.000 description 17
- 239000002245 particle Substances 0.000 description 16
- 239000000463 material Substances 0.000 description 12
- 238000005259 measurement Methods 0.000 description 11
- 230000000694 effects Effects 0.000 description 10
- 238000005242 forging Methods 0.000 description 10
- 238000012545 processing Methods 0.000 description 10
- 238000003490 calendering Methods 0.000 description 9
- 238000005096 rolling process Methods 0.000 description 9
- 235000019362 perlite Nutrition 0.000 description 8
- 239000010451 perlite Substances 0.000 description 8
- 230000009467 reduction Effects 0.000 description 8
- 238000005336 cracking Methods 0.000 description 7
- 239000000203 mixture Substances 0.000 description 7
- 230000008569 process Effects 0.000 description 7
- 238000012797 qualification Methods 0.000 description 6
- 239000000126 substance Substances 0.000 description 6
- 229910052731 fluorine Inorganic materials 0.000 description 5
- 229910052739 hydrogen Inorganic materials 0.000 description 5
- 229910052759 nickel Inorganic materials 0.000 description 5
- 239000006104 solid solution Substances 0.000 description 5
- 238000004458 analytical method Methods 0.000 description 4
- 239000012467 final product Substances 0.000 description 4
- 238000000691 measurement method Methods 0.000 description 4
- 229910052760 oxygen Inorganic materials 0.000 description 4
- 229910052700 potassium Inorganic materials 0.000 description 4
- 238000005491 wire drawing Methods 0.000 description 4
- 238000010276 construction Methods 0.000 description 3
- 238000000354 decomposition reaction Methods 0.000 description 3
- 238000005098 hot rolling Methods 0.000 description 3
- 239000011229 interlayer Substances 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 229910052796 boron Inorganic materials 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 150000001247 metal acetylides Chemical class 0.000 description 2
- 230000003287 optical effect Effects 0.000 description 2
- 238000002161 passivation Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 229910052717 sulfur Inorganic materials 0.000 description 2
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 1
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- 206010033546 Pallor Diseases 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000005054 agglomeration Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 229910052787 antimony Inorganic materials 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 239000010962 carbon steel Substances 0.000 description 1
- 238000005255 carburizing Methods 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 239000010432 diamond Substances 0.000 description 1
- 229910003460 diamond Inorganic materials 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 239000004744 fabric Substances 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 230000005764 inhibitory process Effects 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000012423 maintenance Methods 0.000 description 1
- 230000014759 maintenance of location Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 230000004660 morphological change Effects 0.000 description 1
- OXNIZHLAWKMVMX-UHFFFAOYSA-N picric acid Chemical compound OC1=C([N+]([O-])=O)C=C([N+]([O-])=O)C=C1[N+]([O-])=O OXNIZHLAWKMVMX-UHFFFAOYSA-N 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 230000002035 prolonged effect Effects 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 239000011347 resin Substances 0.000 description 1
- 229920005989 resin Polymers 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
Classifications
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/52—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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
-
- 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
- C21D8/06—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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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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
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/003—Cementite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
Description
本發明係有關作為機械構造零件之材料使用之鋼線。更詳言之,係關於對藉由調質壓延所製造之線材實施球狀化燒鈍後之冷軋加工之際,冷軋加工時之變形阻力低、耐龜裂性良好、且可發揮冷軋加工性優異之特性之機械構造零件用鋼線。又本說明書中,所謂「線材」係以壓延線材之意思使用,係指熱軋壓延後冷卻至室溫之線狀鋼材。且所謂「鋼線」係指對壓延線材施以球狀化燒鈍等之調質處理之線狀鋼材。 The present invention relates to steel wires used as materials for mechanical structural parts. More specifically, in the case of cold rolling processing after spheroidizing and blunting of a wire manufactured by quenching and temper rolling, the deformation resistance during cold rolling is low, the crack resistance is good, and the wire can be cooled. A steel wire for mechanical structural parts with excellent rolling workability. In the present specification, the term "wire material" is used in the sense of a rolled wire, and refers to a linear steel material which is cooled to room temperature after hot rolling and rolling. The term "steel wire" refers to a linear steel material which is subjected to a tempering treatment such as spheroidizing and blunting on a rolled wire.
製造汽車用零件及建設機械用零件等之各種機械構造用零件時,通常對碳鋼及合金鋼等之熱軋壓延線材以賦予冷軋加工性之目的而施以球狀化燒鈍。接著,對球狀化燒鈍後之壓延線材亦即鋼線進行冷軋加工,隨後施以切削加工等之機械加工而成形為特定形狀,並進行淬冷回火且處理最終進行強度調整,作成機械構造用零件。 When manufacturing various parts for mechanical structures such as parts for automobiles and parts for construction machinery, the hot-rolled rolled wires such as carbon steel and alloy steel are usually spheroidally burnt for the purpose of imparting cold-rolling workability. Then, the steel wire which is a spheroidized burnt wire is subjected to cold rolling, and then subjected to machining by cutting or the like to be formed into a specific shape, quenched and tempered, and finally subjected to strength adjustment to prepare. Parts for mechanical construction.
冷軋加工中,藉由降低鋼線之變形阻力,可 期待模具壽命之提高。且藉由提高鋼線之耐龜裂性,可期待各種零件之良率提高。 In cold rolling, by reducing the deformation resistance of the steel wire, Expect an increase in the life of the mold. Moreover, by increasing the crack resistance of the steel wire, it is expected that the yield of various parts will be improved.
迄今,作為提高鋼線之冷軋加工性之技術,已提案有各種方法。作為此種技術,例如專利文獻1中,揭示有如下技術「一種鋼線,其係金屬組織實質上由肥粒鐵粒與球狀碳化物所構成,前述肥粒鐵粒係平均粒徑為15μm以上,前述球狀碳化物係平均粒徑為0.8μm以下,且最大粒徑為4.0μm以下,且每1mm2之個數為0.5×106×C%~5.0×106×C%個,前述球狀碳化物中,粒徑為0.1μm以上之球狀碳化物間之最大距離為10μm以下」。 Heretofore, various methods have been proposed as techniques for improving the cold rolling workability of steel wires. As such a technique, for example, Patent Document 1 discloses a steel wire in which a metal structure consists essentially of ferrite iron particles and spherical carbides, and the average grain size of the ferrite particles is 15 μm. In the above, the spherical carbide-based average particle diameter is 0.8 μm or less, and the maximum particle diameter is 4.0 μm or less, and the number per 1 mm 2 is 0.5 × 10 6 × C% to 5.0 × 10 6 × C%. In the spherical carbide, the maximum distance between the spherical carbides having a particle diameter of 0.1 μm or more is 10 μm or less.
且專利文獻2中揭示如下技術:「一種鋼線,其係鋼的金屬組織具有滲碳體與肥粒鐵,滲碳體與肥粒鐵相對於全部組織之合計面積率為95%以上,並且前述滲碳體之90%以上之長寬比為3以下,且前述滲碳體之平均重心距離為1.5μm以上,進而前述肥粒鐵之平均結晶粒徑為5~20μm」。 Further, Patent Document 2 discloses a technique of "a steel wire in which a metal structure of a steel has cementite and ferrite iron, and a total area ratio of cementite and ferrite iron to all tissues is 95% or more, and The aspect ratio of 90% or more of the cementite is 3 or less, and the average center-of-gravity distance of the cementite is 1.5 μm or more, and the average crystal grain size of the ferrite iron is 5 to 20 μm.
該專利文獻2中,作為獲得上述金屬組織之手段,揭示有於A1點~A1點+50℃之溫度區域升溫,於升溫後於前述A1點~A1點+50℃之溫度區域保持0~1hr後,自前述A1點~A1點+50℃之溫度區域至A1點-100℃~A1點-30℃之溫度區域以10~200℃/hr之平均冷卻速度冷卻之燒鈍處理進行2次以上後,於A1點~A1點+30℃之溫度區域升溫,並於A1點~A1點+30℃之溫度區域保持後冷卻之條件控制如下。亦即,揭示升溫時到達A1點後,於A1 點~A1點+30℃之溫度區域保持後冷卻時,於到達A1點之前之前述A1點~A1點+30℃之溫度區域滯留時間設為10分鐘~2小時,將自前述A1點~A1點+30℃之溫度區域至A1點-100℃~A1點-20℃之冷卻溫度區域以10~100℃/hr之平均冷卻速度冷卻後,於該冷卻溫度區域保持10分鐘~5小時後,進一步冷卻之方法。 In Patent Document 2, as a means for obtaining the above-described metal structure, it is revealed that the temperature is raised in the temperature range from A1 to A1 + 50 ° C, and after the temperature rise, the temperature is maintained at 0 to 1 hr in the temperature range of A1 to A1 + 50 ° C. Then, from the temperature range of A1 point to A1 point +50 °C to the temperature range of A1 point -100 °C~A1 point -30 °C, the blunt cooling treatment is performed at an average cooling rate of 10 to 200 ° C / hr for 2 times or more. Thereafter, the temperature is raised in the temperature range from A1 to A1 + 30 ° C, and the conditions for maintaining the post-cooling in the temperature range of A1 to A1 + 30 ° C are controlled as follows. That is, after the temperature rise reaches A1 point, it is in A1. When the temperature range from point ~A1 +30 °C is maintained and cooled, the retention time in the temperature range from A1 point to A1 point +30 °C before reaching point A1 is set to 10 minutes to 2 hours, from the above point A1~A1 The temperature region from +30 ° C to the cooling temperature region of A1 point -100 ° C ~ A1 point -20 ° C is cooled at an average cooling rate of 10 to 100 ° C / hr, and after maintaining the cooling temperature region for 10 minutes to 5 hours, The method of further cooling.
另一方面,專利文獻3中,揭示如下技術「一種鋼線,其具有將滲碳體間距離之標準偏差除以前述滲碳體間距離之平均值之值為0.50以下之組織」。以該方法,滲碳體大致以均一間隔分佈,且於肥粒鐵粒內亦存在多數滲碳體。 On the other hand, Patent Document 3 discloses a technique of "a steel wire having a structure in which the standard deviation of the distance between cementites is divided by the average value of the distance between the cementites to be 0.50 or less." In this way, cementite is distributed at substantially uniform intervals, and a majority of cementite is also present in the ferrite particles.
[專利文獻1]國際公開第2011/108459號 [Patent Document 1] International Publication No. 2011/108459
[專利文獻2]日本特開2012-140674號公報 [Patent Document 2] Japanese Patent Laid-Open Publication No. 2012-140674
[專利文獻3]日本特開2006-316291號公報 [Patent Document 3] Japanese Laid-Open Patent Publication No. 2006-316291
迄今所提案之技術作為提高冷軋鍛造等之冷軋加工性之鋼線之技術雖有用,但期望開發冷軋加工性更提高之鋼線之技術。 The technology proposed so far is useful as a technique for improving the cold-rolling workability of steel wire such as cold-rolling forging, but it is desired to develop a steel wire having improved cold-rolling workability.
本發明係基於此種狀況完成者,其目的係提 供可實現冷軋加工時之變形阻力減低並且提高耐龜裂性且可發揮優異之冷軋加工性之機械構造零件用鋼線。 The present invention is based on the completion of such a situation, the purpose of which is A steel wire for mechanical structural parts that can reduce the deformation resistance during cold rolling and improve the crack resistance and exhibit excellent cold rolling workability.
達成上述課題之本發明之機械構造零件用鋼線以質量%計,分別含有C:0.3~0.6%、Si:0.05~0.5%、Mn:0.2~1.7%、P:超過0%且0.03%以下、S:0.001~0.05%、Al:0.005~0.1%及N:0~0.015%,其餘部分係由鐵及不可避免雜質所成,鋼的金屬組織係由肥粒鐵及滲碳體構成,存在於肥粒鐵粒界之滲碳體之數量比例相對於全部滲碳體數為40%以上。 The steel wire for the mechanical structural component of the present invention which achieves the above-mentioned problem contains C: 0.3 to 0.6%, Si: 0.05 to 0.5%, Mn: 0.2 to 1.7%, and P: more than 0% and 0.03% or less, respectively, by mass%. , S: 0.001~0.05%, Al: 0.005~0.1% and N: 0~0.015%. The rest is made of iron and inevitable impurities. The metal structure of steel consists of ferrite and cementite. The proportion of cementite in the ferrite grain boundary is 40% or more relative to the total number of cementite.
本發明之機械構造零件用鋼線較好以質量%計,進而含有自以下所成之群選出之1種以上:Cr:超過0%且0.5%以下、Cu:超過0%且0.25%以下、Ni:超過0%且0.25%以下、Mo:超過0%且0.25%以下、及B:超過0%且0.01%以下。 The steel wire for the mechanical structural component of the present invention is preferably one by mass or more, and further contains one or more selected from the group consisting of: Cr: more than 0% and 0.5% or less, and Cu: more than 0% and 0.25% or less. Ni: more than 0% and 0.25% or less, Mo: more than 0% and 0.25% or less, and B: more than 0% and 0.01% or less.
本發明之機械構造零件用鋼線中,較好前述金屬組織中之bcc(body-centered cubic:體心立方晶格)-Fe結晶粒之平均相當圓直徑為30μm以下。 In the steel wire for a mechanical structural part of the present invention, it is preferred that the bcc (body-centered cubic)-Fe crystal grain in the metal structure has an average equivalent circle diameter of 30 μm or less.
依據本發明之機械構造零件用鋼線,藉由將化學成分組成適當調整,並且鋼的金屬組織由肥粒鐵及滲碳體構成,且存在於肥粒鐵粒界之滲碳體之數量比例相對 於全部滲碳體數滿足規定值,可提供可實現變形阻力減低並且耐龜裂性提高之鋼線。本發明之機械構造零件用鋼線由於變形阻力減低,故可抑制模具等之塑性加工用治工具之磨耗及破壞,且由於耐龜裂性提高,故亦可抑制壓造壓工時之龜裂發生,可發揮冷軋加工性優異之特性。 According to the steel wire for mechanical structural parts of the present invention, the chemical composition is appropriately adjusted, and the metal structure of the steel is composed of ferrite iron and cementite, and the proportion of cementite present in the iron grain boundary of the fat grain relatively When the total number of cementites satisfies a predetermined value, a steel wire which can achieve a reduction in deformation resistance and an improved crack resistance can be provided. Since the steel wire for the mechanical structural part of the present invention is reduced in deformation resistance, it is possible to suppress wear and damage of the plastic working tool such as a mold, and since crack resistance is improved, cracking during press working can be suppressed. When it occurs, it can exhibit the characteristics of excellent cold rolling workability.
本發明人等為了實現冷軋加工時之變形阻力減低並且耐龜裂性提高之鋼線而自各種角度進行檢討。其結果,發現於冷軋加工時,肥粒鐵粒內之滲碳體會增加變形阻力,且成為龜裂原因之孔洞會以肥粒鐵粒內之滲碳體為起點。 The inventors of the present invention reviewed various angles in order to realize a steel wire having reduced deformation resistance and improved crack resistance during cold rolling. As a result, it was found that in the cold rolling process, the cementite in the ferrite grains increases the deformation resistance, and the pores which cause the cracks start from the cementite in the ferrite grains.
存在於肥粒鐵粒界之滲碳體與粒內存在之滲碳體相比,由於冷軋加工時所受到之變形量小,故可減低變形阻力,並且可抑制成為孔洞之起點。亦即,得到之設想係為了實現兼具變形阻力減低與耐龜裂性提高,重要的是增大存在於肥粒鐵粒界之滲碳體相對於全部滲碳體數之數量比例,亦即減低存在於肥粒鐵粒內之滲碳體相對於全部滲碳體數之數量比例。 The cementite present in the ferrite grain boundary is smaller than the cementite present in the grain, and the amount of deformation during cold rolling is small, so that the deformation resistance can be reduced and the starting point of the hole can be suppressed. That is, it is assumed that in order to achieve both the deformation resistance reduction and the crack resistance improvement, it is important to increase the proportion of the cementite present in the ferrite grain boundary with respect to the total number of cementites, that is, Reduce the amount of cementite present in the ferrite particles relative to the total number of cementites.
迄今所提案之技術中,提高變形阻力及耐龜裂性之方法已知有控制肥粒鐵粒徑之方法,但並非著眼於累積於粒界之滲碳體者。 Among the techniques proposed so far, a method of controlling the deformation resistance and the crack resistance is known as a method of controlling the particle size of the ferrite, but it is not focused on the cementite accumulated in the grain boundary.
以下針對本發明所規定之各要件加以說明。 The various requirements specified in the present invention are described below.
本發明之機械構造零件用鋼線(以下有時簡稱 為「鋼線」)之金屬組織為所謂之球狀化組織,係由肥粒鐵及滲碳體構成。上述球狀化組織係有助於減低鋼的變形阻力且提高冷軋加工性之金屬組織。本發明之金屬組織中,亦可一部分含有珍珠岩組織。且,若對於冷軋加工性帶來之不良影響小,則AlN等之析出物以面積率計可容許未達3%。 Steel wire for mechanical structural parts of the present invention (hereinafter sometimes referred to as abbreviated The metal structure of the "steel wire" is a so-called spheroidized structure composed of ferrite iron and cementite. The spheroidized structure contributes to reducing the deformation resistance of steel and improving the metal structure of cold rolling workability. In the metal structure of the present invention, a part of the metal structure may also contain a perlite structure. Further, if the adverse effect on the cold rolling workability is small, the precipitate such as AlN can be allowed to be less than 3% in terms of the area ratio.
然而,僅成為簡單由肥粒鐵及滲碳體構成之金屬組織,無法實現冷軋加工性之提高。由此,如以下所詳述般,該金屬組織中之存在於肥粒鐵粒界之滲碳體相對於全部滲碳體數之數量比例有必要適當控制。 However, it is only a metal structure composed of ferrite iron and cementite, and it is impossible to improve the cold rolling workability. Therefore, as described in detail below, it is necessary to appropriately control the amount ratio of the cementite present in the iron grain boundary of the ferrite grain to the total number of cementite in the metal structure.
又,本說明書中,存在於肥粒鐵粒界之滲碳體(粒界滲碳體)相對於全部滲碳體數之數量比例稱為「粒界滲碳體比例」。又,存在於肥粒鐵粒內之滲碳體(粒內滲碳體)相對於全部滲碳體數之數量比例稱為「粒內滲碳體比例」。「粒界滲碳體比例」及「粒內滲碳體比例」如下述般定義。 Further, in the present specification, the ratio of the amount of cementite (grain boundary cementite) present in the ferrite grain boundary to the total number of cementite is referred to as "grain boundary cementite ratio". Further, the ratio of the amount of cementite (granular cementite) present in the ferrite grains to the total number of cementites is referred to as "the ratio of intragranular cementite". The "grain boundary cementite ratio" and "granular cementite ratio" are defined as follows.
金屬組織之顯微鏡觀察中,於特定視野內以特定方法分別測量粒界滲碳體與粒內滲碳體數。 In the microscopic observation of the metal structure, the number of grain boundary cementite and the number of intragranular cementite were measured by a specific method in a specific field of view.
將粒界滲碳體之數設為“Na”,粒內滲碳體之數設為“Nb”及全部滲碳體數(粒界滲碳體數與粒內滲碳體數之合計)設為“Na+Nb”時,粒界滲碳體比例與粒內滲碳體比例可如以下般求得。 The number of grain boundary cementite is "Na", the number of cementite in the grain is set to "Nb" and the total number of cementite (the total number of cementites in the grain boundary and the number of cementite in the grain) When it is "Na+Nb", the ratio of the grain boundary cementite to the intragranular cementite can be obtained as follows.
粒界滲碳體比例(%)=Na/(Na+Nb)×100 Grain boundary cementite ratio (%) = Na / (Na + Nb) × 100
粒內滲碳體比例(%)=Nb/(Na+Nb)×100 Proportion of intragranular cementite (%) = Nb / (Na + Nb) × 100
滲碳體數之測量可於一視野進行,亦可於複數視野進行。於複數視野進行測量時,係使用各視野所測量之粒界滲碳體數與粒內滲碳體數各者合計之數值,算出粒界滲碳體比例與粒內滲碳體比例。 The measurement of the number of cementite can be carried out in one field of view or in multiple fields of view. When measuring in the plural field of view, the ratio of the number of grain boundary cementites to the number of intragranular cementites measured by each field of view is used to calculate the ratio of grain boundary cementite to intragranular cementite.
測量方法之細節於後述。 The details of the measurement method will be described later.
粒界滲碳體比例減低,粒內滲碳體比例增加時,冷軋加工中導入肥粒鐵粒之錯位偏移至粒內滲碳體,引起錯位增加,顯示加工硬化。結果,變形阻力增加,冷軋加工性降低。且粒內滲碳體與粒界滲碳體相比,在冷軋加工中於滲碳體周圍容易堆積變形。其結果,粒內滲碳體容易成為龜裂之起點。由此,於肥粒鐵粒界上析出滲碳體對於提高冷軋加工性極為有效。 When the proportion of cementite in the grain boundary is reduced and the proportion of cementite in the grain increases, the misalignment of the ferrite particles introduced into the cold rolling process shifts to the intragranular cementite, causing an increase in dislocation and showing work hardening. As a result, the deformation resistance increases and the cold rolling workability decreases. Moreover, the intragranular cementite tends to be deposited and deformed around the cementite in the cold rolling process as compared with the grain boundary cementite. As a result, the intragranular cementite tends to be the starting point of the crack. Therefore, precipitation of cementite on the ferrite grain boundary is extremely effective for improving cold rolling workability.
由此等觀點,存在於肥粒鐵粒界之滲碳體之數量比例(亦即粒界滲碳體比例)相對於全部滲碳體數必須為40%以上。藉由將粒界滲碳體比例設為40%以上,可減低變形阻力,抑制滲碳體起點之龜裂發生。 From this point of view, the proportion of cementite present in the ferrite grain boundary (ie, the ratio of grain boundary cementite) must be 40% or more relative to the total number of cementite. By setting the grain boundary cementite ratio to 40% or more, the deformation resistance can be reduced, and cracking of the cementite origin can be suppressed.
成為粒界滲碳體數及粒內滲碳體數之測定對象之滲碳體形態並未特別限定。例如除了球狀滲碳體以外,包含長寬比較大之棒狀之滲碳體及形成珍珠岩組織之層狀之滲碳體等,並未限制於滲碳體之形狀。又,成為測定對象之滲碳體大小並未限定,但係由測定方法決定大小之基準。後述之粒界滲碳體比例之測定方法可將可藉由倍率1000倍之光學顯微鏡判別之滲碳體之尺寸設為最小尺寸。具體而言,以相當圓直徑為0.3μm以上之尺寸的滲碳 體為測定對象。 The morphology of the cementite to be measured for the number of grain boundary cementite and the number of intragranular cementite is not particularly limited. For example, in addition to the spherical cementite, the cementite including the rod-like cementite having a relatively large length and a large width and the layered cementite forming the perlite structure are not limited to the shape of the cementite. Further, the size of the cementite to be measured is not limited, but the size is determined by the measurement method. The method for measuring the ratio of the grain boundary cementite described later can be set to a minimum size by the size of the cementite which can be discriminated by an optical microscope at a magnification of 1000 times. Specifically, carburizing is performed in a size having a substantially circular diameter of 0.3 μm or more. The body is the object of measurement.
粒界滲碳體比例之較佳下限為45%,更好為50%。粒界滲碳體比例越高,變形阻力減低、龜裂抑制越有效,最好為100%。但,如後述之粒界滲碳體比例增加就製造面而言並不容易,以現狀之技術,可能有熱軋壓延溫度降低及/或球狀化燒鈍時間長時間化等之缺點。現行技術中基於製造性之觀點,粒界滲碳體比例較好約80%以下,更好為70%以下。 The preferred lower limit of the ratio of grain boundary cementite is 45%, more preferably 50%. The higher the ratio of grain boundary cementite, the lower the deformation resistance and the more effective the crack inhibition, preferably 100%. However, the increase in the proportion of the grain boundary cementite described later is not easy in terms of the production surface, and there is a possibility that the hot rolling calendering temperature is lowered and/or the spheroidizing blunt time is prolonged due to the current state of the art. In the prior art, the ratio of the grain boundary cementite is preferably about 80% or less, more preferably 70% or less, based on the viewpoint of manufacturability.
本發明之鋼線中,前述金屬組織中之bcc-Fe結晶粒之平均相當圓直徑較好為30μm以下。藉由將bcc-Fe結晶粒之平均相當圓直徑(以下有時簡稱為「bcc-Fe結晶粒徑」)為30μm以下,可提高延展性,更抑制冷軋加工時之龜裂發生。bcc-Fe結晶粒徑之較加上限為25μm,更好為20μm。又,成為測定對象之bcc-Fe結晶粒之大小並未限定,與前述滲碳體同樣,根據測定方法決定大小之基準。於後述之測定方法,將可藉由EBPS解析裝置及FE-SEM判別之尺寸設為最小尺寸。具體而言,相當圓直徑為1μm以上之尺寸的bcc-Fe結晶粒為測定對象。 In the steel wire according to the present invention, the average equivalent circle diameter of the bcc-Fe crystal grains in the metal structure is preferably 30 μm or less. By setting the average equivalent circular diameter of the bcc-Fe crystal grains (hereinafter sometimes abbreviated as "bcc-Fe crystal grain size") to 30 μm or less, ductility can be improved, and cracking during cold rolling can be suppressed. The upper limit of the bcc-Fe crystal grain size is 25 μm, more preferably 20 μm. Moreover, the size of the bcc-Fe crystal grain to be measured is not limited, and the size of the material is determined in accordance with the measurement method as in the case of the cementite. In the measurement method described later, the size which can be determined by the EBPS analysis device and the FE-SEM is set to the minimum size. Specifically, a bcc-Fe crystal grain having a size of a circle having a diameter of 1 μm or more is a measurement object.
成為前述之bcc-Fe結晶粒徑之控制對象之組織係由方位差大於15°之較大之大角粒界所包圍之bcc-Fe結晶粒。其理由係前述方位差為15°以下之小角粒界時,對冷軋加工性所帶來之影響較小。又,前述之「結晶方位差」亦稱為「錯開角」或「傾角」,方位差之測定只要採用EBSP法(Electron Backscattering Pattern法)即可。且, 測定平均粒徑之由大角粒界包圍之bcc-Fe除了初析肥粒鐵以外,亦包含在珍珠岩組織中所含之肥粒鐵。 The structure to be controlled by the above-mentioned bcc-Fe crystal grain size is a bcc-Fe crystal grain surrounded by a large large-angle grain boundary having a difference in orientation of more than 15°. The reason for this is that when the azimuth difference of 15° or less is small, the influence on the cold rolling workability is small. Further, the above-mentioned "crystal orientation difference" is also referred to as "shift angle" or "tilt angle", and the measurement of the azimuth difference may be performed by the EBSP method (Electron Backscattering Pattern method). And, The bcc-Fe surrounded by the large-angle grain boundary, which measures the average particle diameter, contains the ferrite iron contained in the perlite structure in addition to the initial precipitated iron.
本發明係以機械構造零件之材料中所用之鋼線為對象者,只要具有作為機械構造零件用鋼線之通常化學成分組成即可,但關於C、Si、Mn、P、S、Al及N宜調整於適當範圍內。基於此種觀點,該等化學成分之適當範圍及其限定理由如下述。又,本說明書中,關於化學成分組成所稱「%」之意指質量%。 The present invention is directed to a steel wire used in a material of a mechanical structural part, as long as it has a usual chemical composition as a steel wire for a mechanical structural part, but regarding C, Si, Mn, P, S, Al, and N. Should be adjusted to the appropriate range. Based on this point of view, the appropriate range of such chemical components and the reasons for their limitation are as follows. In the present specification, the term "%" as used in the chemical composition means mass%.
C係確保鋼之強度亦即最終製品之強度上有用之元素。為了有效發揮此效果,C含量有必要設為0.3%以上。C含量較好為0.32%以上,更好為0.34%以上。然而,C若過量含有則強度變高冷軋加工性降低,故有必要設為0.6%以下。C含量較好為0.55%以下,更好為0.50%以下。 The C system is an element that ensures the strength of the steel, that is, the strength of the final product. In order to effectively exert this effect, it is necessary to set the C content to 0.3% or more. The C content is preferably 0.32% or more, more preferably 0.34% or more. However, if C is excessively contained, the strength becomes high and the cold rolling workability is lowered. Therefore, it is necessary to set it to 0.6% or less. The C content is preferably 0.55% or less, more preferably 0.50% or less.
Si係作為脫氧元素,及係藉由固熔體硬化而增加最終製品強度為目的而含有者。為了有效發揮此效果,Si含量定為0.05%以上。Si含量較好為0.07%以上,更好為0.10%以上。另一方面,Si若過量含有則硬度過度上升使冷軋加工性劣化。因此Si含量定為0.5%以下。Si含量較好為0.45%以下,更好為0.40%以下。 The Si system is contained as a deoxidizing element and is intended to increase the strength of the final product by solid solution hardening. In order to effectively exert this effect, the Si content is set to be 0.05% or more. The Si content is preferably 0.07% or more, more preferably 0.10% or more. On the other hand, if Si is excessively contained, the hardness is excessively increased to deteriorate the cold rolling workability. Therefore, the Si content is set to be 0.5% or less. The Si content is preferably 0.45% or less, more preferably 0.40% or less.
Mn係藉由淬冷性提高而增加最終製品強度之有效元素。為了有效發揮此效果,Mn含量定為0.2%以上。Mn含量較好為0.3%以上,更好為0.4%以上。另一方面Mn若過量含有,則硬度上升且冷軋加工性劣化。因此Mn含量定為1.7%以下。Mn含量較好為1.5%以下,更好為1.3%以下。 Mn is an effective element for increasing the strength of the final product by improving the quenching property. In order to effectively exert this effect, the Mn content is set to 0.2% or more. The Mn content is preferably 0.3% or more, more preferably 0.4% or more. On the other hand, when Mn is excessively contained, the hardness increases and the cold rolling workability deteriorates. Therefore, the Mn content is set to 1.7% or less. The Mn content is preferably 1.5% or less, more preferably 1.3% or less.
P係鋼中不可避免含有之元素,於鋼中成為引起粒界偏析、延展性劣化之原因。因此P含量定為0.03%以下。P含量較好為0.02%以下,更好為0.017%以下,特佳為0.01%以下。P含量若少則越少越好,根據製造步驟上之限制亦有殘存0.001%左右之情況。 An element that is inevitably contained in the P-based steel causes a segregation of the grain boundary and deterioration of ductility in the steel. Therefore, the P content is set to be 0.03% or less. The P content is preferably 0.02% or less, more preferably 0.017% or less, and particularly preferably 0.01% or less. If the P content is small, the smaller the better, and the remaining amount may be about 0.001% depending on the limitation of the production steps.
S係鋼中不可避免含有之元素,於鋼中作為MnS存在而使延展性劣化,故係對冷軋加工性有害之元素。因此S含量定為0.05%以下。S含量較好為0.04%以下,更好為0.03%以下。但由於S具有提高被削性之作用,故含有0.001%以上。S含量較好為0.002%以上,更好為0.003%以上。 An element which is inevitably contained in the S-based steel, which is present as MnS in steel and deteriorates ductility, is an element harmful to cold-rolling workability. Therefore, the S content is set to be 0.05% or less. The S content is preferably 0.04% or less, more preferably 0.03% or less. However, since S has an effect of improving the machinability, it contains 0.001% or more. The S content is preferably 0.002% or more, more preferably 0.003% or more.
Al係作為脫氧元素而有用並且於將鋼中存在之固熔N作為AlN予以固定時有用。為了有效發揮此效果,Al含量定為0.005%以上。Al含量較好為0.008%以上,更好為0.010%以上。然而,Al含量若過量,則Al2O3過量生成,使冷軋加工性劣化。因此Al含量定為0.1%以下。Al含量較好為0.090%以下,更好為0.080%以下。 Al is useful as a deoxidizing element and is useful when the solid solution N existing in steel is fixed as AlN. In order to effectively exert this effect, the Al content is set to be 0.005% or more. The Al content is preferably 0.008% or more, more preferably 0.010% or more. However, when the Al content is excessive, Al 2 O 3 is excessively formed to deteriorate the cold rolling workability. Therefore, the Al content is set to be 0.1% or less. The Al content is preferably 0.090% or less, more preferably 0.080% or less.
N係鋼中不可避免含有之元素,若於鋼中含有固熔N,則因變形時效而使硬度上升,導致延展性降低,使冷軋加工性劣化。因此N含量定為0.015%以下。N含量較好為0.013%以下,更好為0.010%以下。N含量若少則越少越好,最好為0%,因製造步驟上之限制等亦有殘存0.001%左右之情況。 An element which is inevitably contained in the N-based steel. When the steel contains a solid-melting N, the hardness is increased by the deformation aging, and the ductility is lowered to deteriorate the cold-rolling workability. Therefore, the N content is set to be 0.015% or less. The N content is preferably 0.013% or less, more preferably 0.010% or less. If the N content is small, the less is preferably as small as possible, and it is preferably 0%, and the residual amount in the manufacturing step may be about 0.001%.
本發明之鋼線之基本成分如上述,其餘部分實質上為鐵。又,所謂「實質上為鐵」意指除了鐵以外亦容許不阻礙本發明特性程度之微量成分(例如Sb及Zn等),亦可包含P、S及N以外之不可避免雜質(例如O及H等)。進而本發明中,亦可根據需要含有以下任意元素,根據所含有之成分而進一步改善鋼線特性。 The basic components of the steel wire of the present invention are as described above, and the remainder is substantially iron. In addition, "substantially iron" means that a small amount of components (for example, Sb and Zn) which do not inhibit the characteristics of the present invention, in addition to iron, may be contained, and may also contain inevitable impurities other than P, S and N (for example, O and H, etc.). Further, in the present invention, any of the following elements may be contained as needed, and the characteristics of the steel wire may be further improved depending on the components contained therein.
自以下所成之群選出之1種以上:Cr:超過0%且0.5%以下、Cu:超過0%且0.25%以下、Ni:超過0%且0.25%以下、Mo:超過0%且0.25%以下、及B:超 過0%且0.01%以下 One or more selected from the group consisting of: Cr: more than 0% and 0.5% or less, Cu: more than 0% and 0.25% or less, Ni: more than 0% and 0.25% or less, Mo: more than 0% and 0.25% Below, and B: Super Over 0% and below 0.01%
Cr、Cu、Ni、Mo及B均係藉由提高鋼材之淬冷性而增加最終製品強度之有效元素,可根據需要以單獨或2種以上含有。此等效果係隨著該等元素含量增加而變大,為了有效發揮前述效果之較佳含量係Cr量為0.015%以上,更好為0.020%以上。Cu量、Ni量及Mo量之較佳含量均為0.02%以上,更好為0.05%以上。B量之較佳含量為0.0003%以上,更好為0.0005%以上。 Each of Cr, Cu, Ni, Mo, and B is an effective element for increasing the strength of the final product by improving the quenching property of the steel material, and may be contained alone or in combination of two or more kinds as needed. These effects are increased as the content of the elements increases, and the amount of Cr is preferably 0.015% or more, more preferably 0.020% or more, in order to effectively exhibit the above effects. The content of Cu, the amount of Ni, and the amount of Mo are preferably 0.02% or more, more preferably 0.05% or more. The content of B is preferably 0.0003% or more, more preferably 0.0005% or more.
然而,Cr、Cu、Ni、Mo及B之含量若過量,則強度過於提高且冷軋加工性劣化。因此,Cr量較好為0.5%以下,Cu、Ni及Mo含量較好均為0.25%以下,B之含量較佳為0.01%以下。該等元素之更佳含量係Cr量為0.45%以下,更好為0.40%以下。Cu、Ni及Mo量之更佳上限均為0.22%,更好為0.20%。B量之更佳上限為0.007%,更好為0.005%。 However, if the content of Cr, Cu, Ni, Mo, and B is excessive, the strength is excessively increased and the cold rolling workability is deteriorated. Therefore, the amount of Cr is preferably 0.5% or less, and the contents of Cu, Ni, and Mo are preferably 0.25% or less, and the content of B is preferably 0.01% or less. A more preferable content of the elements is such that the amount of Cr is 0.45% or less, more preferably 0.40% or less. A more preferable upper limit of the amounts of Cu, Ni and Mo is 0.22%, more preferably 0.20%. The upper limit of the amount of B is preferably 0.007%, more preferably 0.005%.
本發明之鋼線係規定球狀化燒鈍後之組織形態者,為了成為此種組織形態,較好適當控制後述之球狀化燒鈍條件。但,為了確保如上述之組織形態,更好進而在製造壓延線材之階段之條件亦適當控制,而使壓延線材中之組織形態在球狀化燒鈍時成為易析出粒界滲碳體之狀態。 In the steel wire system of the present invention, it is preferable to appropriately control the spheroidizing burn-off condition to be described later in order to obtain the shape of the structure after the spheroidizing burnt. However, in order to secure the above-described texture, it is better to control the conditions at the stage of producing the rolled wire, and the state of the microstructure in the rolled wire becomes a state in which grain boundary cementite is easily precipitated when spheroidized and burnt. .
於壓延線材製造階段,滿足上述成分組成之鋼較好係調整熱軋壓延時之精加工壓延溫度同時將隨後之冷卻速度作為3階段適當調整冷卻速度及溫度範圍。藉由 以此等條件製造壓延線材,可使球狀化燒鈍前之組織以珍珠岩及肥粒鐵作為主相並且將bcc-Fe結晶粒徑設為特定範圍,且使初析肥粒鐵結晶粒等軸化,且將珍珠岩之最狹窄部分之間隔設為特定以下。藉由對此種組織後述條件進行球狀化燒鈍,容易獲得粒界滲碳體充分析出之鋼線。因此之壓延線材製造條件具體而言,於800℃以上、1050℃以下精加工壓延後,較好依序進行如下之冷卻:平均冷卻速度為7℃/秒以上之第1冷卻、平均冷卻速度為1℃/秒以上、5℃/秒以下之第2冷卻、及平均冷卻速度快於前述第2冷卻且為5℃/秒以上之第3冷卻。前述第1冷卻之結束溫度與前述第2冷卻之起始溫度較好在700~750℃之範圍內。前述第2冷卻之結束溫度與前述第3冷卻之起始溫度較好在600~650℃之範圍內。前述第3冷卻之結束溫度較好為400℃以下。分別針對精加工壓延溫度及第1~3冷卻加以說明。 In the production stage of the rolled wire, the steel satisfying the above composition is preferably adjusted for the finishing rolling temperature of the hot rolling pressing delay, and the subsequent cooling rate is appropriately adjusted as the three stages to adjust the cooling rate and the temperature range. By By manufacturing the calendered wire under such conditions, the spheroidized blunt tissue can be made of perlite and ferrite iron as the main phase and the bcc-Fe crystal grain size can be set to a specific range, and the initial precipitated iron crystal grain can be obtained. It is equiaxed, and the interval between the narrowest portions of the perlite is set to be specific or less. By spheroidizing and burning the conditions described later for this type of structure, it is easy to obtain a steel wire which is analyzed by the grain boundary cementite. Therefore, after the calendering wire production conditions are specifically 800° C. or more and 1050° C. or less, the following cooling is preferably performed in sequence: the first cooling rate and the average cooling rate are 7° C./sec or more. The second cooling of 1 ° C / sec or more and 5 ° C / sec or less and the third cooling of the average cooling rate faster than the second cooling and 5 ° C / sec or more. The end temperature of the first cooling and the initial temperature of the second cooling are preferably in the range of 700 to 750 °C. The temperature at which the second cooling is completed and the initial temperature of the third cooling are preferably in the range of 600 to 650 °C. The temperature at which the third cooling is completed is preferably 400 ° C or lower. The finishing rolling temperature and the first to third cooling will be described separately.
為了減小球狀化燒鈍前之組織之bcc-Fe結晶粒徑例如為15μm以下,較好適當控制精加工壓延溫度。精加工壓延溫度超過1050℃時,難以使bcc-Fe結晶粒徑減小。但,精加工壓延溫度未達800℃時,bcc-Fe結晶粒徑過小,例如未達5μm而難以軟質化,故較好設為800℃以上。精加工壓延溫度之更佳下限為850℃,更好為900℃以上。精加工壓延溫度之更佳上限為1000℃,更好為950 ℃。 In order to reduce the particle diameter of the bcc-Fe crystal of the structure before the spheroidizing blunt, for example, 15 μm or less, it is preferred to appropriately control the finishing calendering temperature. When the finishing rolling temperature exceeds 1050 ° C, it is difficult to reduce the particle diameter of the bcc-Fe crystal. However, when the finishing rolling temperature is less than 800 ° C, the bcc-Fe crystal grain size is too small, for example, it is less than 5 μm and it is difficult to soften, so it is preferably 800 ° C or more. A lower limit of the finishing calendering temperature is 850 ° C, more preferably 900 ° C or more. The upper limit of the finishing calendering temperature is 1000 ° C, more preferably 950 °C.
第1冷卻係自精加工壓延溫度的800℃以上、1050℃以下開始,於700~750℃之溫度範圍結束。該第1冷卻中,冷卻速度若變慢,則有球狀化燒鈍前之組織之bcc-Fe結晶粒粗大化,bcc-Fe結晶粒徑變大之虞。因此,第1冷卻之平均冷卻速度較好設為7℃/秒以上。第1冷卻之平均冷卻速度更好為10℃/秒以上,又更好為20℃/秒以上。第1冷卻之平均冷卻速度之上限並未特別限制,但作為現實之範圍較好為200℃/秒以下。又,第1冷卻之冷卻只要平均冷卻速度為7℃/秒以上,則亦可使冷卻速度變化而冷卻。 The first cooling system is started at a temperature ranging from 700 to 750 ° C from 800 ° C to 1050 ° C from the finishing rolling temperature. In the first cooling, when the cooling rate is slow, the bcc-Fe crystal grains of the structure before the spheroidal blunt are coarsened, and the bcc-Fe crystal grain size becomes large. Therefore, the average cooling rate of the first cooling is preferably set to 7 ° C / sec or more. The average cooling rate of the first cooling is more preferably 10 ° C / sec or more, and still more preferably 20 ° C / sec or more. The upper limit of the average cooling rate of the first cooling is not particularly limited, but the range of reality is preferably 200 ° C / sec or less. Further, in the cooling of the first cooling, if the average cooling rate is 7 ° C /sec or more, the cooling rate may be changed and cooled.
第2冷卻係自700~750℃之溫度範圍開始,於600~650℃之溫度範圍結束。為了使初析肥粒鐵結晶粒等軸化,亦即使初析肥粒鐵結晶粒之平均長寬比減小例如為3.0以下,於第2冷卻中,較好以5℃/秒以下之平均冷卻速度緩慢冷卻。第2冷卻之平均冷卻速度之更佳上限為4℃/秒,更好為3.5℃/秒以下。另一方面,第2冷卻之平均冷卻速度若過慢,則有bcc-Fe結晶粒粗大化,bcc-Fe結晶粒徑變得過大之可能性。因此,第2冷卻之平均冷卻速度較好為1℃/秒以上。第2冷卻之平均冷卻速度之更佳 下限為2℃/秒,更好為2.5℃/秒。又,第2冷卻之冷卻,只要平均冷卻速度為1℃/秒以上、5℃/秒以下,則亦可使冷卻速度變化而冷卻。 The second cooling system starts at a temperature range of 700 to 750 ° C and ends at a temperature range of 600 to 650 ° C. In order to make the initial precipitated iron crystal grains equiaxed, the average aspect ratio of the primary precipitated iron crystal grains is reduced to, for example, 3.0 or less, and in the second cooling, the average is preferably 5 ° C/second or less. The cooling rate is slowly cooled. A more preferable upper limit of the average cooling rate of the second cooling is 4 ° C / sec, more preferably 3.5 ° C / sec or less. On the other hand, if the average cooling rate of the second cooling is too slow, the bcc-Fe crystal grains may be coarsened, and the bcc-Fe crystal grain size may become excessively large. Therefore, the average cooling rate of the second cooling is preferably 1 ° C /sec or more. Better average cooling rate for the second cooling The lower limit is 2 ° C / sec, more preferably 2.5 ° C / sec. Further, in the cooling of the second cooling, if the average cooling rate is 1 ° C / sec or more and 5 ° C / sec or less, the cooling rate may be changed and cooled.
第3冷卻係自600~650℃之溫度範圍開始,於400℃以下結束。該第3冷卻係為使珍珠岩之平均層間間隔僅可能狹小,使滲碳體易於溶解,不於粒內殘留球狀滲碳體之核。藉此,藉由進行隨後之適當球狀化燒鈍處理,而增加粒界滲碳體比例。為使珍珠岩之平均層間間隔狹小例如為0.20μm以下,第3冷卻中,較好快於第2冷卻且以5℃/秒以上之平均冷卻速度冷卻。若以慢於5℃/秒冷卻則不易使珍珠岩之平均層間間隔狹小。第3冷卻之平均冷卻速度更好為10℃/秒以上,又更好為20℃/秒以上。 The third cooling system starts from a temperature range of 600 to 650 ° C and ends below 400 ° C. The third cooling system is such that the average interlayer spacing of the perlite is only narrow, so that the cementite is easily dissolved, and the core of the spherical cementite remains in the particles. Thereby, the grain boundary cementite ratio is increased by performing the subsequent appropriate spheroidization blanching treatment. In order to make the average interlayer interval of the perlite narrow, for example, 0.20 μm or less, in the third cooling, it is preferably faster than the second cooling and cooled at an average cooling rate of 5 ° C /sec or more. If the cooling is slower than 5 ° C / sec, it is not easy to make the average interlayer spacing of the perlite narrow. The average cooling rate of the third cooling is more preferably 10 ° C / sec or more, and still more preferably 20 ° C / sec or more.
又,第3冷卻之平均冷卻速度之上限並未特別限定,但較好為現實範圍之200℃/秒以下。又,第3冷卻中,只要平均冷卻速度為5℃/秒以上,則亦可使冷卻速度變化而冷卻。第3冷卻之結束溫度之下限並未特別限定,但較好為例如200℃。進行第3冷卻後,只要進行放冷等之通常冷卻而冷卻至室溫即可。 Further, the upper limit of the average cooling rate of the third cooling is not particularly limited, but is preferably 200 ° C / sec or less in the actual range. Further, in the third cooling, if the average cooling rate is 5 ° C /sec or more, the cooling rate may be changed and cooled. The lower limit of the end temperature of the third cooling is not particularly limited, but is preferably, for example, 200 °C. After the third cooling, it is sufficient to cool to room temperature by cooling normally or the like.
冷卻至室溫後,亦可根據需要進而於室溫進行伸線加工,此時之減面率設為例如30%以下即可。伸線時,由於鋼中之碳化物被破壞,於隨後之球狀化燒鈍可促進碳化物之凝集,故可有效縮短球狀化燒鈍之均熱處理時 間。但,伸線加工之減面率若超過30%,則由於會有燒鈍後之強度變高冷軋加工性劣化之虞,故伸線加工之減面率較好為30%以下。又,減面率之下限並未特別限定,較好藉由設為2%以上而獲得效果。 After cooling to room temperature, the wire drawing process may be further performed at room temperature as needed, and the reduction ratio may be, for example, 30% or less. When the wire is stretched, since the carbide in the steel is destroyed, the subsequent spheroidization can promote the agglomeration of the carbide, so that the uniform heat treatment of the spheroidized burnt blunt can be effectively shortened. between. However, if the reduction ratio of the wire drawing process exceeds 30%, the strength after cold burning becomes high and the cold rolling workability deteriorates. Therefore, the reduction ratio of the wire drawing process is preferably 30% or less. Further, the lower limit of the reduction ratio is not particularly limited, and it is preferred to obtain an effect by setting it to 2% or more.
以如上述之較佳條件製造之壓延線材,藉由隨後之球狀化燒鈍處理,而使組織中之珍珠岩形態變化為奧氏體(austenite),隨後與肥粒鐵+滲碳體之形態變化中,使原本之珍珠岩尺寸變小,亦即抑制金屬組織之粒成長,而可減低滲碳體之粒內析出,成為易析出粒界滲碳體之狀態。 The calendered wire produced by the above-mentioned preferred conditions is subjected to subsequent spheroidizing blunt treatment to change the morphology of the perlite in the structure to austenite, followed by the ferrite iron + cementite In the morphological change, the original perlite size is reduced, that is, the grain growth of the metal structure is suppressed, and the precipitation of the cementite in the grain is reduced, and the state of the grain boundary cementite is easily precipitated.
作為如此之球狀化燒鈍條件,較好對於壓延線材,於例如後述之SA1般,於大氣爐中自室溫加熱至730℃時,至少自500℃至730℃係以平均加熱速度50℃/小時以上加熱,隨後以平均加熱速度2~5℃/小時加熱至740℃,於740℃保持1~3小時後,以平均冷卻速度20℃/小時以上冷卻至720℃,以平均冷卻速度8~12℃/小時冷卻至640℃,隨後放冷。 As such a spheroidizing and blunt condition, it is preferred that the rolled wire is heated at a temperature of from room temperature to 730 ° C in an atmospheric furnace, for example, as described later, at an average heating rate of 50 ° C from at least 500 ° C to 730 ° C. Heating for more than one hour, then heating to 740 ° C at an average heating rate of 2 to 5 ° C / hour, holding at 740 ° C for 1-3 hours, cooling to an average cooling rate of 20 ° C / hour or more to 720 ° C, with an average cooling rate of 8 ~ Cool to 640 ° C at 12 ° C / hour, then let cool.
上述之球狀化燒鈍條件中,自室溫加熱至730℃時,藉由至少自500℃至730℃之平均加熱速度設為50℃/小時以上,而抑制金屬組織之粒成長。此時之平均加熱速度更好為60℃/小時以上。然而,平均加熱速度過快時,壓延線材之溫度追隨變困難,故較好設為200℃/小時以下,更好為150℃/小時以下。 In the spheroidizing blunt condition described above, when heating from room temperature to 730 ° C, the average heating rate from at least 500 ° C to 730 ° C is 50 ° C / hour or more, thereby suppressing grain growth of the metal structure. The average heating rate at this time is more preferably 60 ° C / hour or more. However, when the average heating rate is too fast, the temperature of the rolled wire becomes difficult to follow, and therefore it is preferably 200 ° C / hour or less, more preferably 150 ° C / hour or less.
又,自室溫加熱至500℃時之平均加熱速度通 常為100℃/小時以上,於該溫度範圍之平均加熱速度對金屬組織之粒成長帶來之影響較小。若考慮生產性,此時之加熱速度較快較好,例如為120℃/小時以上,更好為140℃/小時以上。此時之平均加熱速度上限,與自500℃至730℃之平均加熱速度同樣,較好設為200℃/小時,更好為150℃/小時。自室溫加熱至500℃時之平均加熱速度可至少與自500℃至730℃之平均加熱速度相同亦可不同。總之,藉由減小原先之珍珠岩尺寸,而可減低滲碳體之粒內析出,成為易析出粒界滲碳體之狀態,故只要至少自500℃至730℃之平均加熱速度確保為50℃/小時以上即可。 Moreover, the average heating rate when heated from room temperature to 500 ° C Usually 100 ° C / hour or more, the average heating rate in this temperature range has little effect on the grain growth of the metal structure. In consideration of productivity, the heating rate at this time is preferably faster, for example, 120 ° C / hour or more, more preferably 140 ° C / hour or more. The upper limit of the average heating rate at this time is preferably 200 ° C / hour, more preferably 150 ° C / hour, as the average heating rate from 500 ° C to 730 ° C. The average heating rate when heated from room temperature to 500 ° C may be at least the same as the average heating rate from 500 ° C to 730 ° C. In short, by reducing the size of the original perlite, the precipitation of cementite in the grain can be reduced, and the state of the grain boundary cementite is easily precipitated, so that the average heating rate of at least from 500 ° C to 730 ° C is guaranteed to be 50. °C / hour or more can be.
且藉由將A1點正上方之自730℃至740℃之平均加熱速度控制在2~5℃/小時,可邊極力抑制金屬組織之粒成長,邊充分進行珍珠岩組織中之滲碳體之分解及固熔。平均加熱速度快於5℃/小時時,難以確保珍珠岩組織中之滲碳體之分解及固熔之充分時間,平均加熱速度慢於2℃/小時時,自730℃至740℃之加熱時間變長,變得難以控制金屬組織之粒成長。此時之平均加熱速度更好為3℃/小時以上、4℃/小時以下。 And by controlling the average heating rate from 730 ° C to 740 ° C directly above the A1 point to 2 to 5 ° C / hr, it is possible to suppress the growth of the metal structure as much as possible while sufficiently performing the cementite in the perlite structure. Decomposition and solid solution. When the average heating rate is faster than 5 ° C / hour, it is difficult to ensure sufficient time for the decomposition and solid solution of cementite in the perlite structure, and the average heating rate is slower than 2 ° C / hour, and the heating time is from 730 ° C to 740 ° C. It becomes longer and becomes difficult to control the growth of the grain of the metal structure. The average heating rate at this time is more preferably 3 ° C / hour or more and 4 ° C / hour or less.
較好於740℃保持1~3小時。該保持溫度若短於1小時,則珍珠岩組織中之滲碳體之分解及固熔不充分,若長於3小時,則難以抑制金屬組織之粒成長。此時之保持時間更好為1.5小時以上、2.5小時以下。 It is preferably maintained at 740 ° C for 1 to 3 hours. When the holding temperature is shorter than 1 hour, decomposition and solid solution of cementite in the perlite structure are insufficient, and if it is longer than 3 hours, it is difficult to suppress grain growth of the metal structure. The holding time at this time is preferably 1.5 hours or more and 2.5 hours or less.
如上述般進行保持後,藉由將直至720℃之較 佳平均冷卻速度設為20℃/小時以上,可抑制金屬組織之粒成長。此時之平均冷卻速度更好為30℃/小時以上,但平均冷卻速度過快時,由於壓延線材之溫度追隨變困難,故較好設為100℃/小時以下。 After maintaining as above, by comparing to 720 ° C The optimum average cooling rate is set to 20 ° C / hour or more, and the growth of the metal structure can be suppressed. The average cooling rate at this time is more preferably 30 ° C /hr or more. However, when the average cooling rate is too fast, the temperature of the rolled wire is difficult to follow, and therefore it is preferably 100 ° C /hr or less.
隨後,藉由將自720℃至640℃之平均冷卻速度控制在8~12℃/小時,可於肥粒鐵粒界優先析出滲碳體,而可抑制如珍珠岩組織般之長寬比大的滲碳體析出。平均冷卻速度慢於8℃/小時時,金屬組織之粒成長之抑制困難,平均冷卻速度快於12℃/小時時,如珍珠岩組織般之長寬比大的滲碳體大量再析出。此時之平均冷卻速度更好為9℃/小時以上、11℃/小時以下。 Subsequently, by controlling the average cooling rate from 720 ° C to 640 ° C to 8 to 12 ° C / hour, cementite can be preferentially precipitated in the ferrite grain boundary, and the aspect ratio as large as the perlite structure can be suppressed. The cementite precipitates. When the average cooling rate is slower than 8 ° C / hour, the growth of the grain growth of the metal structure is difficult, and when the average cooling rate is faster than 12 ° C / hour, a large amount of cementite having a large aspect ratio like a perlite structure is reprecipitated. The average cooling rate at this time is more preferably 9 ° C / hour or more and 11 ° C / hour or less.
如上述之球狀化燒鈍可進行複數次,藉由如此重複進行,可減小滲碳體各個之長寬比,增加粒界滲碳體比例。例如,如後述之實施例之試驗No.7、12、14、19及27所示般,即使使用未適當控制壓延線材製造條件之鋼種C、E、F、H及K時,隨後藉由重複進行特定球狀化燒鈍,亦可使粒界滲碳體比例成為適當範圍內,可減低變形阻力及龜裂發生率兩者。 As described above, the spheroidizing blunt can be performed plural times, and by repeating this, the aspect ratio of the cementite can be reduced, and the ratio of the grain boundary cementite can be increased. For example, as shown in Test Nos. 7, 12, 14, 19, and 27 of the examples described later, even if the steel grades C, E, F, H, and K which are not properly controlled for the production conditions of the rolled wire are used, they are subsequently repeated. When the specific spheroidization is performed, the ratio of the grain boundary cementite can be made to an appropriate range, and both the deformation resistance and the crack occurrence rate can be reduced.
關於球狀化燒鈍之重複次數較好至少3次以上,但由於過度操作粒界滲碳體比例亦無太大變化,故較好為10次以下。又,重複複數次球狀化鈍化時,在上述較佳條件之範圍下,可以相同條件重複,亦可以不同條件重複。 The number of repetitions of the spheroidized burnt blunt is preferably at least three or more, but since the ratio of the excessively manipulated grain boundary cementite does not change much, it is preferably 10 or less. Further, when the spheroidal passivation is repeated a plurality of times, it may be repeated under the same conditions within the above-described preferable conditions, or may be repeated under different conditions.
以下,列舉實施例更具體說明本發明。本發明不受以下實施例之限制,當然在可適於前述、後述之主旨之範圍內可加入適當變更而實施,該等均包含於本發明之技術範圍。 Hereinafter, the present invention will be more specifically described by way of examples. The present invention is not limited to the following examples, and it is to be understood that the invention can be carried out with appropriate modifications within the scope of the present invention.
使用下述表1所示之化學成分組成之鋼,以下述表2之各種製造條件進行壓延,製作 17.0mm之線材。表2中,冷卻1、冷卻2及冷卻3對應於本發明推薦之第1冷卻、第2冷卻及第3冷卻。鋼種B係化學成分組成偏離規定值之比較例。 The steel having the chemical composition shown in Table 1 below was rolled and produced under various production conditions shown in Table 2 below. 17.0mm wire. In Table 2, cooling 1, cooling 2, and cooling 3 correspond to the first cooling, the second cooling, and the third cooling recommended by the present invention. A comparative example in which the chemical composition of the steel B system deviates from the predetermined value.
鋼種C、E、F、H、K、O、P及Q係並非以本發明之適當製造條件製造壓延線材之例。該等鋼種C、E、F及K之精加工壓延溫度變高。且鋼種H係與第3冷卻對應之冷卻3的冷卻速度慢之條件,亦即維持第2冷卻之冷卻速度之狀態冷卻而製造壓延線材之例。 The steel grades C, E, F, H, K, O, P and Q are not examples of producing rolled wires under the appropriate manufacturing conditions of the present invention. The finishing calendering temperatures of the steel grades C, E, F and K become high. Further, the steel type H is cooled under the condition that the cooling rate of the cooling 3 corresponding to the third cooling is slow, that is, the state in which the cooling rate of the second cooling is maintained, and the rolled wire is produced.
鋼種O係進行第2冷卻至550℃後,加熱至580℃,進行於580℃保持120秒之保持步驟,放冷至室溫進行減面率40%之伸線加工步驟。且鋼種P係僅以冷卻1之單調冷卻速度進行冷卻。鋼種Q係進行冷卻1後,進行於550℃保持60秒之保持步驟,放冷至室溫進行減面率15%之粗伸線。 The steel type O was subjected to a second cooling to 550 ° C, then heated to 580 ° C, and maintained at 580 ° C for 120 seconds, and allowed to cool to room temperature to carry out a wire drawing processing step of 40% reduction. The steel grade P is cooled only by the monotonic cooling rate of cooling 1. After the steel type Q was cooled 1, the holding step was carried out at 550 ° C for 60 seconds, and the mixture was allowed to cool to room temperature to carry out a thick drawing line having a reduction ratio of 15%.
其次,對於鋼種O、P及Q以外之各壓延線材,以大氣爐,進行下述之任一者:(a)自室溫加熱至730℃之際,自室溫至500℃係以平均加熱速度110℃/小時,自500℃至730℃係以平均加熱速度80℃/小時加熱,隨後以平均加熱溫度3℃/小時加熱至740℃,於740℃保持3小時後,以平均冷卻速度30℃/小時冷卻至720℃,以平均冷卻速度10℃/小時冷卻至640℃,隨後放冷之球狀化燒鈍(該燒鈍條件以下簡稱為「SA1」),(b)重複5次之SA1(該燒鈍條件於以下簡稱為「SA2」)及(c)自室溫加熱至730℃之際,自室溫至500℃係以平均加熱速度110℃/小時,自500℃至730℃係以平均加熱速度80℃/小時加熱,隨後以平均加熱溫度3℃/小時加熱至740℃,於740℃保持3小時後,以平均冷卻速度30℃/小時冷卻至640℃,隨後放冷之球狀化燒鈍(該燒鈍條件以下簡稱為「SA3」)。上述燒鈍條件SA1及SA2為本發明之較佳燒鈍條件,上述燒鈍條件SA3係自720℃至640℃之平均冷卻速度未適當控制之例。 Next, for each of the rolled wires other than the steel types O, P, and Q, the following furnace is used: (a) heating from room temperature to 730 ° C, from room temperature to 500 ° C at an average heating rate of 110 °C / hour, from 500 ° C to 730 ° C is heated at an average heating rate of 80 ° C / hour, then heated to 740 ° C at an average heating temperature of 3 ° C / hour, held at 740 ° C for 3 hours, with an average cooling rate of 30 ° C / After cooling to 720 ° C in an hour, it was cooled to 640 ° C at an average cooling rate of 10 ° C / hour, and then spheroidized and burnt by cooling (the blunt condition is hereinafter referred to as "SA1"), (b) SA1 repeated 5 times ( The blunt condition is hereinafter referred to as "SA2") and (c) heating from room temperature to 730 ° C, from room temperature to 500 ° C at an average heating rate of 110 ° C / hour, from 500 ° C to 730 ° C for average heating The temperature was heated at 80 ° C / hour, then heated to 740 ° C at an average heating temperature of 3 ° C / hour, held at 740 ° C for 3 hours, cooled to 640 ° C at an average cooling rate of 30 ° C / hour, and then cooled and spheroidized. Blunt (this blunt condition is hereinafter referred to as "SA3"). The above-mentioned blunt conditions SA1 and SA2 are preferred blunt conditions of the present invention, and the above-mentioned blunt condition SA3 is an example in which the average cooling rate from 720 ° C to 640 ° C is not properly controlled.
又,對於鋼種O,以大氣爐,進行下述之任一者:(d)以平均加熱速度80℃/小時自室溫加熱至680℃,於680℃保持5小時後,以平均冷卻速度10℃/小時冷卻至640℃,隨後放冷之球狀化燒鈍(該燒鈍條件以下簡稱為「SA4」)及(e)以平均加熱速度80℃/小時自室溫加熱至700℃,於700℃保持5小時後,以平均冷卻速度10℃/小時冷卻至640℃,隨後放冷之球狀化燒鈍(該燒鈍條件以 下簡稱為「SA5」)。上述燒鈍條件SA4及SA5為偏離本發明之較佳燒鈍條件之例。 Further, for the steel type O, in the atmospheric furnace, one of the following is performed: (d) heating from room temperature to 680 ° C at an average heating rate of 80 ° C / hour, and maintaining at 680 ° C for 5 hours, at an average cooling rate of 10 ° C /hour cooling to 640 ° C, followed by cooling spheroidal burning blunt (the blunt condition is hereinafter referred to as "SA4") and (e) heating at room temperature to 700 ° C at an average heating rate of 80 ° C / hour, at 700 ° C After 5 hours of maintenance, it was cooled to 640 ° C at an average cooling rate of 10 ° C / hour, and then spheroidized and blunt-cooled (the blunt condition was Hereinafter referred to as "SA5"). The above-mentioned blunt conditions SA4 and SA5 are examples which deviate from the preferred blunt conditions of the present invention.
且對於鋼種P,以大氣爐,進行下述之任一者:(f)以平均加熱速度80℃/小時自室溫加熱至740℃,隨後立即以平均冷卻速度80℃/小時冷卻至660℃,該等步驟重複3次(但第二次以後自660℃開始加熱),隨後以平均加熱速度80℃/小時自660℃加熱至740℃,於740℃保持30分鐘後,以平均冷卻速度80℃/小時冷卻至660℃,於660℃保持1小時,隨後放冷之球狀化燒鈍(該燒鈍條件以下簡稱為「SA6」)及(g)以平均加熱速度80℃/小時自室溫加熱至740℃,於740℃保持10分鐘後,以平均冷卻速度80℃/小時冷卻至660℃,該步驟重複3次(但第二次以後自660℃開始加熱),隨後以平均加熱速度80℃/小時自660℃加熱至740℃,於740℃保持30分鐘後,以平均冷卻速度80℃/小時冷卻至660℃,於660℃保持1小時,隨後放冷之球狀化燒鈍(該燒鈍條件以下簡稱為「SA7」)。上述燒鈍條件SA6及SA7為偏離本發明之較佳燒鈍條件之例。 And for the steel species P, in an atmospheric furnace, any one of the following: (f) heating from room temperature to 740 ° C at an average heating rate of 80 ° C / hour, and then immediately cooling to 660 ° C at an average cooling rate of 80 ° C / hour, These steps were repeated 3 times (but heated from 660 ° C after the second time), then heated from 660 ° C to 740 ° C at an average heating rate of 80 ° C / hour, and maintained at 740 ° C for 30 minutes, at an average cooling rate of 80 ° C. /hour cooling to 660 ° C, maintaining at 660 ° C for 1 hour, followed by cooling spheroidal burning blunt (the blunt condition is hereinafter referred to as "SA6") and (g) heating at room temperature at an average heating rate of 80 ° C / hour After maintaining at 740 ° C for 10 minutes at 740 ° C, it was cooled to 660 ° C at an average cooling rate of 80 ° C / hour. This step was repeated 3 times (but after 260 ° C after the second time), followed by an average heating rate of 80 ° C. /hour heated from 660 ° C to 740 ° C, after maintaining at 740 ° C for 30 minutes, cooled to 660 ° C at an average cooling rate of 80 ° C / hour, held at 660 ° C for 1 hour, and then chilled spheroidized burnt (the burn) The blunt condition is hereinafter referred to as "SA7"). The above-mentioned blunt conditions SA6 and SA7 are examples which deviate from the preferred blunt conditions of the present invention.
對於鋼種Q,以大氣爐,進行下述之任一者:(h)以平均加熱速度150℃/小時自室溫加熱至720℃,於720℃保持1小時後,放冷之球狀化燒鈍(該燒鈍條件以下簡稱為「SA8」)及(i)以平均加熱速度150℃/小時自室溫加熱至730℃,於730℃保持1小時後,放冷之球狀化燒鈍(該燒鈍條件以下簡稱為「SA9」)。上述燒鈍條件 SA8及SA9為偏離本發明之較佳燒鈍條件之例。 For the steel type Q, in an atmospheric furnace, one of the following is performed: (h) heating from room temperature to 720 ° C at an average heating rate of 150 ° C / hour, holding at 720 ° C for 1 hour, and then cooling the spheroidized blunt (The blunt condition is hereinafter referred to as "SA8") and (i) heating from room temperature to 730 ° C at an average heating rate of 150 ° C / hour, and maintaining at 730 ° C for 1 hour, then cooling the spheroidized blunt (the burning) The blunt condition is hereinafter referred to as "SA9"). The above blunt condition SA8 and SA9 are examples of preferred blunt conditions that deviate from the present invention.
針對進行上述球狀化燒鈍後之鋼線,藉下述方法測定(1)金屬組織之bcc-Fe結晶粒徑,(2)粒界滲碳體比例,(3)冷軋加工時之變形阻力及(4)冷軋加工時之龜裂發生率。 For the steel wire after the spheroidization and blunting, the following methods are used to determine (1) the bcc-Fe crystal grain size of the metal structure, (2) the grain boundary cementite ratio, and (3) the deformation during the cold rolling process. Resistance and (4) Cracking rate during cold rolling.
又,球狀化燒鈍後之鋼線之肥粒鐵粒徑及粒界滲碳體比例之測定時,以可觀察橫剖面之方式埋入樹脂,藉由磨砂布紙及鑽石拋光而鏡面研磨切剖面。對於鋼線之半徑D,測定距鋼線表面為D/4之位置。 In addition, in the measurement of the grain size of the ferrite iron and the ratio of the grain boundary cementite in the spheroidized blunt steel wire, the resin is embedded in an observable cross section, and mirror-polished by sanding cloth and diamond polishing. Cut the section. For the radius D of the steel wire, the position from the surface of the steel wire is measured as D/4.
bcc-Fe結晶粒徑之測定係使用EBSP解析裝置及FE-SEM(場發射掃描電子顯微鏡,電解放出型掃描電子顯微鏡)進行測定。解析工具係使用TSL Solution股份有限公司之OIM軟體。將結晶方位差(此亦稱為「斜角」)超過15之邊界亦即大角粒界作為結晶粒界定義「結晶粒」,算出將bcc-Fe結晶粒之面積換算為圓時之直徑之平均值亦即平均相當圓之直徑。此時之測定區域設為200μm×400μm,測定步階設為1.0μm間隔,顯示測定方位之信賴性之信賴指數(Confidence Index)為0.1以下之測定點自解析對象刪除。 The measurement of the bcc-Fe crystal grain size was carried out by using an EBSP analysis apparatus and an FE-SEM (field emission scanning electron microscope, electro-emission type scanning electron microscope). The analysis tool uses OIM software from TSL Solution Co., Ltd. The average of the diameters when the area of the bcc-Fe crystal grain is converted into a circle is calculated by defining the crystal grain boundary as a boundary of the crystal grain boundary with a crystal orientation difference (this is also called "oblique angle") exceeding the boundary of 15. The value is also the diameter of the average equivalent circle. In this case, the measurement area is set to 200 μm×400 μm, the measurement step is set to 1.0 μm, and the measurement point indicating that the reliability index of the measurement orientation is 0.1 or less is deleted from the analysis target.
粒界滲碳體比例之測定中,藉由5分鐘以上之苦味酸 浸蝕呈現出肥粒鐵粒界及滲碳體,以光學顯微鏡進行組織觀察,以倍率1000倍拍攝3視野。於該等照片上,劃出等間隔之10條橫線,測定該線上存在之粒界滲碳體數及粒內滲碳體數。將3視野內存在之粒界滲碳體數除以同視野內存在之全部滲碳體數,而算出粒界滲碳體比例。所測定之滲碳體之最小相當圓之直徑設為0.3μm。此處,與肥粒鐵粒界接觸且滲碳體粒子之長寬比為3.0以下者定義為粒界滲碳體。因此,即使與肥粒鐵粒界接觸,滲碳體粒子之長寬比超過3.0者設為粒內滲碳體。 In the determination of the ratio of grain boundary cementite, picric acid by more than 5 minutes The etch showed a ferrite grain boundary and a cementite, and the tissue was observed by an optical microscope, and three fields of view were taken at a magnification of 1000 times. On these photographs, 10 horizontal lines at equal intervals were drawn, and the number of grain boundary cementite and the number of intragranular cementite present on the line were measured. The ratio of grain boundary cementite in the three fields of view is divided by the total number of cementites present in the same field of view to calculate the ratio of grain boundary cementite. The diameter of the smallest equivalent circle of the cementite measured was set to 0.3 μm. Here, it is defined as grain boundary cementite in contact with the ferrite grain boundary and the aspect ratio of the cementite particles is 3.0 or less. Therefore, even if it is in contact with the ferrite grain boundary, the aspect ratio of the cementite particles exceeding 3.0 is set as the granular cementite.
自鋼線製作 10.0mm×15.0mm之冷軋鍛造試驗用樣品,使用鍛造加壓,於室溫以變形速度5/秒~10/秒,各進行5次加工率60%之冷軋鍛造試驗。變形阻力之測定係自由60%加工率之冷軋鍛造試驗所得之加工率-變形阻力之數據,測定5次40%加工時之變形阻力,求出5次之平均值。又,C含量為0.3~未達0.4%之範圍內之鋼種A~E及P之變形阻力之合格基準為650MPa以下。C含量為0.4~未達0.5%之範圍內之鋼種F~J、O及Q之變形阻力之合格基準為680MPa以下。C含量為0.5~未達0.6%之範圍內之鋼種K~N之變形阻力之合格基準為730MPa以下。 Steel wire production A cold-rolling forging test sample of 10.0 mm × 15.0 mm was subjected to a cold-rolling forging test at a processing rate of 60% at a deformation rate of 5/sec to 10/sec at room temperature using forging pressurization. The measurement of the deformation resistance is the data of the processing rate-deformation resistance obtained by the cold-rolling forging test of 60% of the processing rate, and the deformation resistance at the time of the 40% processing was measured five times, and the average value of the five times was obtained. Further, the qualification standard of the deformation resistance of the steel grades A to E and P in the range of the C content of 0.3 to less than 0.4% is 650 MPa or less. The qualification standard for the deformation resistance of the steel grades F~J, O and Q in the range of 0.4% to less than 0.5% is 680 MPa or less. The qualification standard for the deformation resistance of the steel type K to N in the range of 0.5 to less than 0.6% is 730 MPa or less.
自鋼線製作 10.0mm×15.0mm之冷軋鍛造試驗用樣 品,使用鍛造加壓,於室溫以變形速度5/秒~10/秒,各進行5次加工率60%之冷軋鍛造試驗。龜裂發生率之測定係於60%加工率之冷軋鍛造試驗後,各以實體顯微鏡進行5次表面觀察,以倍率20倍測定表面龜裂之有無,以「表面有龜裂之樣品數」除以5而求得其平均。所有鋼種之龜裂發生率之合格基準為20%以下。 Steel wire production A cold-rolling forging test sample of 10.0 mm × 15.0 mm was subjected to a cold-rolling forging test at a processing rate of 60% at a deformation rate of 5/sec to 10/sec at room temperature using forging pressurization. The cracking rate was measured after a cold-rolling forging test of 60% processing rate, and each surface observation was performed five times with a solid microscope, and the presence or absence of surface cracks was measured at a magnification of 20 times, and the number of samples having cracks on the surface was measured. Divide by 5 to find the average. The pass rate for cracking of all steel grades is less than 20%.
該等結果與球狀化燒鈍條件一起示於下表3。又,表3之綜合評價欄中,變形阻力之減低及耐龜裂性提高均良好之例表示為「O.K」,變形阻力之減低及耐龜裂性提高之至少一者劣化之例表示為「N.G」。 These results are shown in Table 3 below together with the spheroidized burn-off conditions. In the comprehensive evaluation column of Table 3, the example in which the deformation resistance is reduced and the crack resistance is improved is "OK", and the example in which at least one of the deformation resistance is reduced and the crack resistance is improved is indicated as " NG".
由表3之結果可探討如下。試驗No.1、2、7~9、12、14~16、19~21、23、24、27~29、31、32、34 及35係滿足本發明規定之全部要件之實施例,可知同時達成變形阻力之減低及耐龜裂性提高。 The results from Table 3 can be discussed as follows. Test No. 1, 2, 7~9, 12, 14~16, 19~21, 23, 24, 27~29, 31, 32, 34 And 35 are examples in which all the requirements of the present invention are satisfied, and it is understood that the deformation resistance is reduced and the crack resistance is improved at the same time.
該等試驗No.7、12、14、19及27係使用並非以較佳壓延線材條件製造之鋼種C、E、F、H或K之例,但藉由隨後之重複進行之SA2之燒鈍充分析出粒界滲碳體,變形阻力及龜裂發生率均達到合格基準。其中,試驗No.12雖為比較佳要件的bcc-Fe結晶粒徑稍大,但變形阻力及龜裂發生率均達到合格基準。 These Test Nos. 7, 12, 14, 19 and 27 use examples of steels C, E, F, H or K which are not manufactured under the conditions of preferred calendering wire conditions, but are subsequently blunt by repeated repetition of SA2. The grain boundary cementite was analyzed and analyzed, and the deformation resistance and crack occurrence rate all reached the qualified standard. Among them, Test No. 12 is a relatively good material, and the bcc-Fe crystal grain size is slightly larger, but the deformation resistance and the crack occurrence rate all meet the qualification criteria.
此處,若著眼於進行SA1及SA2之燒鈍條件兩者之試驗No.1及2(鋼種A)、試驗No.6及7(鋼種C)、試驗No.8及9(鋼種D)、試驗No.11及12(鋼種E)、試驗No.13及14(鋼種F)、試驗No.15及16(鋼種G)、試驗No.18及19(鋼種H)、試驗No.20及21(鋼種I)、試驗No.23及24(鋼種J)、試驗No.26及27(鋼種K)、試驗No.28及29(鋼種L)、試驗No.31、32(鋼種M)、及試驗No.34及35(鋼種N),可知任一情況與進行SA1之燒鈍的試料相比,進行重複5次SA1的SA2之燒鈍的試料,更可減低變形阻力及龜裂發生率兩者。 Here, attention is paid to tests No. 1 and 2 (steel type A), test Nos. 6 and 7 (steel type C), and test No. 8 and 9 (steel type D) for performing the blunt conditions of SA1 and SA2, Test No. 11 and 12 (steel type E), test No. 13 and 14 (steel type F), test No. 15 and 16 (steel type G), test No. 18 and 19 (steel type H), test No. 20 and 21 (steel type I), test No. 23 and 24 (steel type J), test No. 26 and 27 (steel type K), test No. 28 and 29 (steel type L), test No. 31, 32 (steel type M), and Test No. 34 and 35 (steel type N), it can be seen that in any case, the blunt test of SA2 in which SA1 is repeated five times is performed, and the deformation resistance and the crack occurrence rate can be reduced. By.
相對於此,試驗No.3~6、10、11、13、17、18、22、25、26、30、33及36~42係缺乏本發明規定之要件之任一者的比較例,可知變形阻力及龜裂發生率任一者或兩者未達合格基準。 On the other hand, Test Nos. 3 to 6, 10, 11, 13, 17, 18, 22, 25, 26, 30, 33, and 36 to 42 are comparative examples lacking any of the requirements of the present invention, and it is known that Either or both of the deformation resistance and the crack occurrence rate do not meet the qualification criteria.
亦即,試驗No.3、10、17、22、25、30、33及36係條件非適當而以SA3進行球狀鈍化之例,粒界滲 碳體比例不足,變形阻力及龜裂發生率任一者或兩者未達合格基準。 That is, the test No. 3, 10, 17, 22, 25, 30, 33, and 36 are not suitable for the case of spherical passivation with SA3, grain boundary seepage The carbon body ratio is insufficient, and either or both of the deformation resistance and the crack occurrence rate fail to meet the qualification criteria.
試驗No.4及5係使用Mn含量過量之鋼種B之例,係冷軋加工時之變形阻力高者。 Test Nos. 4 and 5 are examples in which steel type B having an excessive Mn content is used, and the deformation resistance at the time of cold rolling processing is high.
試驗No.6、11、13、18及26係使用非以壓延線材製造時之較佳條件製造之鋼種C、E、F、H或鋼種K之例,藉由隨後之SA1之球形化燒鈍不析出粒界滲碳體,變形阻力及龜裂發生率均未達合格基準。然而,對於該等鋼種,若隨後施以重複5次SA1的SA2之球狀化燒鈍,則成為粒界滲碳體適當析出之狀態,變形阻力及龜裂發生率均達合格基準(試驗No.7、12、14、19及27)。 Test Nos. 6, 11, 13, 18 and 26 are examples of steel grades C, E, F, H or steel K which are not produced by the preferred conditions for the production of rolled wire, by subsequent spheroidization of SA1 No grain boundary cementite was precipitated, and the deformation resistance and crack occurrence rate did not reach the qualified standard. However, in the case of these steel grades, if the spheroidal blunt of SA2 is repeated five times, the grain boundary cementite is appropriately precipitated, and the deformation resistance and the crack occurrence rate are both up to the acceptable standard (Test No. .7, 12, 14, 19 and 27).
試驗No.37及38係使用非以壓延線材製造時之較佳條件製造之鋼種O,以條件非適當之SA4或SA5進行球狀化燒鈍之例,係微細滲碳體均一分散,粒界滲碳體比例變小,變形阻力高,龜裂發生率超過合格基準。 Test Nos. 37 and 38 are examples in which the steel species O produced by the preferred conditions in the production of the rolled wire is spheroidized by the unsuitable SA4 or SA5, and the fine cementite is uniformly dispersed, and the grain boundary is used. The proportion of cementite is small, the deformation resistance is high, and the crack occurrence rate exceeds the qualified standard.
試驗No.39及40係使用非以壓延線材製造時之較佳條件製造之鋼種P,以條件非適當之SA6或SA7進行球狀化燒鈍之例,於肥粒鐵粒內,分散有以於球狀化燒鈍中分斷之層狀滲碳體作為核而球狀化之滲碳體,粒界滲碳體比例變小,變形阻力高,龜裂發生率超過合格基準。 Test Nos. 39 and 40 are examples in which the steel grade P produced by the preferred conditions in the production of the rolled wire material is spheroidized and burnt by the unsuitable SA6 or SA7, and dispersed in the ferrite iron particles. The layered cementite which is divided into spheroidized blunt as a nucleus and spheroidized cementite has a small proportion of grain boundary cementite, high deformation resistance, and the occurrence rate of crack exceeds the qualified standard.
試驗No.41及42係使用非以壓延線材製造時之較佳條件製造之鋼種Q,以條件非適當之SA8或SA9進行球狀化燒鈍之例,大量生成壓延時分斷之層狀滲碳 體,球狀化燒鈍後之粒界滲碳體比例變小,變形阻力高,龜裂發生率超過合格基準。 Test Nos. 41 and 42 used a steel type Q which was not produced under the preferable conditions in the production of a rolled wire, and spheroidized burnt blunt with an unsuitable SA8 or SA9, and a large amount of layered seepage of a time-delayed fracture was formed. carbon After the spheroidized blunt, the ratio of grain boundary cementite becomes small, the deformation resistance is high, and the crack occurrence rate exceeds the qualified standard.
本發明之機械構造零件用鋼線可較好地使用於藉由冷軋鍛造、冷軋壓造及冷壓延等之冷軋加工而製造之汽車用零件及建設機械用零件等之各種機械構造零件之材料。作為此種機械構造零件,具體舉例為機械零件及電器零件等,更具體為螺栓、螺絲、螺帽、套管、球接頭、內管、扭桿、離合箱、殼體、外殼、集線器、外蓋、盒體、調整墊圈、挺桿、座板、barugu、內盒、離合器、套筒、外座圈、鏈齒輪、蕊芯、定子、鐵砧、星形輪、搖臂、機身(body)、法蘭、滾筒、接頭、連接器、滑輪、金屬配件、軛鐵、金屬蓋、起閥器、火星塞、差速小齒輪、轉向軸、共軌(common rail)等。本發明之鋼線可作為上述之機械構造零件之材料適當使用之高強度機械構造零件用鋼線而為產業上有用,於製造上述各種機械構造用零件時之於室溫之變形阻力低,且材料龜裂受抑制而可發揮冷軋加工性。 The steel wire for a machine structural part of the present invention can be preferably used for various mechanical structural parts such as automobile parts and construction machine parts manufactured by cold rolling processing such as cold rolling forging, cold rolling and cold rolling. Material. Specific examples of such mechanical structural components include mechanical parts and electrical parts, and more specifically bolts, screws, nuts, bushings, ball joints, inner tubes, torsion bars, clutch boxes, housings, housings, hubs, and the like. Cover, box body, adjusting washer, tappet, seat plate, barugu, inner box, clutch, sleeve, outer race, chain gear, core, stator, anvil, star wheel, rocker arm, body ), flanges, rollers, joints, connectors, pulleys, metal fittings, yokes, metal covers, valve lifters, spark plugs, differential pinions, steering shafts, common rails, etc. The steel wire of the present invention is industrially useful as a steel wire for high-strength mechanical structural parts which is suitably used as a material of the above-mentioned mechanical structural component, and has low deformation resistance at room temperature when manufacturing various mechanical structural components described above, and Material cracking is suppressed and cold rolling workability can be exhibited.
本申請案係以申請日為2015年3月31日的日本國專利申請、特願第2015-073776號為基礎申請案並主張優先權。特願第2015-073776號藉由參考而併入本說明書中。 The present application is based on the Japanese Patent Application No. 2015-073776, filed on March 31, 2015, and the priority is filed. Japanese Patent Application No. 2015-073776 is incorporated herein by reference.
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TWI808699B (en) * | 2021-03-31 | 2023-07-11 | 日商神戶製鋼所股份有限公司 | Steel wire for mechanical structural parts and manufacturing method thereof |
TWI812127B (en) * | 2021-03-31 | 2023-08-11 | 日商神戶製鋼所股份有限公司 | Steel wire for mechanical structural parts and manufacturing method thereof |
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JP2017106048A (en) * | 2015-12-07 | 2017-06-15 | 株式会社神戸製鋼所 | Steel wire for machine structural component |
TWI635186B (en) * | 2016-10-11 | 2018-09-11 | 新日鐵住金股份有限公司 | Steel wire and coated steel wire |
TWI663266B (en) * | 2017-02-28 | 2019-06-21 | 日商杰富意鋼鐵股份有限公司 | Wire for cutting |
KR102085077B1 (en) * | 2017-12-26 | 2020-03-05 | 주식회사 포스코 | Medium carbon steel wire rod, processed good using the same, and methods for manufacturing thereof |
WO2022210126A1 (en) | 2021-03-31 | 2022-10-06 | 株式会社神戸製鋼所 | Steel wire for machine structural component and manufacturing method thereof |
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JP5618917B2 (en) * | 2011-06-23 | 2014-11-05 | 株式会社神戸製鋼所 | Machine structural steel for cold working, method for producing the same, and machine structural parts |
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2015
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- 2016-03-16 EP EP16772311.3A patent/EP3279355A4/en not_active Withdrawn
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- 2016-03-16 WO PCT/JP2016/058379 patent/WO2016158428A1/en active Application Filing
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TW201341538A (en) * | 2011-12-19 | 2013-10-16 | Kobe Steel Ltd | Steel for mechanical structure for cold working, and method for manufacturing same |
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TWI808699B (en) * | 2021-03-31 | 2023-07-11 | 日商神戶製鋼所股份有限公司 | Steel wire for mechanical structural parts and manufacturing method thereof |
TWI812127B (en) * | 2021-03-31 | 2023-08-11 | 日商神戶製鋼所股份有限公司 | Steel wire for mechanical structural parts and manufacturing method thereof |
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KR20170118902A (en) | 2017-10-25 |
US20180105894A1 (en) | 2018-04-19 |
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EP3279355A4 (en) | 2018-09-05 |
MX2017012063A (en) | 2018-02-09 |
JP6479538B2 (en) | 2019-03-06 |
WO2016158428A1 (en) | 2016-10-06 |
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EP3279355A1 (en) | 2018-02-07 |
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