KR100328039B1 - A Method Manufacturing Wire Rods for cold Heading - Google Patents
A Method Manufacturing Wire Rods for cold Heading Download PDFInfo
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- KR100328039B1 KR100328039B1 KR1019970053795A KR19970053795A KR100328039B1 KR 100328039 B1 KR100328039 B1 KR 100328039B1 KR 1019970053795 A KR1019970053795 A KR 1019970053795A KR 19970053795 A KR19970053795 A KR 19970053795A KR 100328039 B1 KR100328039 B1 KR 100328039B1
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- 238000004519 manufacturing process Methods 0.000 title claims abstract description 14
- 238000000034 method Methods 0.000 title abstract description 11
- 238000010438 heat treatment Methods 0.000 claims abstract description 32
- 238000001816 cooling Methods 0.000 claims abstract description 19
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 8
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 6
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 4
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 4
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 4
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 3
- 238000005096 rolling process Methods 0.000 claims description 26
- 229910052698 phosphorus Inorganic materials 0.000 claims description 3
- 238000003825 pressing Methods 0.000 claims description 2
- 229910000831 Steel Inorganic materials 0.000 abstract description 48
- 239000010959 steel Substances 0.000 abstract description 47
- 229910052757 nitrogen Inorganic materials 0.000 abstract description 8
- 238000005098 hot rolling Methods 0.000 abstract description 5
- 238000003303 reheating Methods 0.000 abstract description 2
- 239000000463 material Substances 0.000 description 23
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 12
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 9
- 229910001567 cementite Inorganic materials 0.000 description 8
- 229910001566 austenite Inorganic materials 0.000 description 7
- 239000010936 titanium Substances 0.000 description 7
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 5
- 238000005097 cold rolling Methods 0.000 description 5
- 239000011572 manganese Substances 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 229910000859 α-Fe Inorganic materials 0.000 description 5
- NRTOMJZYCJJWKI-UHFFFAOYSA-N Titanium nitride Chemical compound [Ti]#N NRTOMJZYCJJWKI-UHFFFAOYSA-N 0.000 description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 229910001562 pearlite Inorganic materials 0.000 description 3
- 238000005482 strain hardening Methods 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 229910000954 Medium-carbon steel Inorganic materials 0.000 description 2
- 238000000137 annealing Methods 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 238000005261 decarburization Methods 0.000 description 2
- 239000012467 final product Substances 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- 238000009825 accumulation Methods 0.000 description 1
- 238000010622 cold drawing Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000004904 shortening Methods 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- 238000004804 winding Methods 0.000 description 1
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B3/02—Rolling special iron alloys, e.g. stainless steel
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/16—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling wire rods, bars, merchant bars, rounds wire or material of like small cross-section
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/16—Control of thickness, width, diameter or other transverse dimensions
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
-
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B2261/00—Product parameters
- B21B2261/20—Temperature
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B2265/00—Forming parameters
- B21B2265/14—Reduction rate
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- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Chemical & Material Sciences (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
Description
본 발명은 볼트, 너트용 소재로 사용되는 냉간압조용 선재의 제조방법에 관한 것으로써, 보다 상세하게는 선재압연을 고온에서 하더라도 강선재 상태의 조직을 미세화시켜 구상화열처리 시간을 비약적으로 단축할 수 있는 냉간압조용 선재의 제조방법에 관한 것이다.The present invention relates to a method for manufacturing a cold-rolled wire rod used as a material for bolts and nuts, and more specifically, even when the wire is rolled at a high temperature, the structure of the steel wire state can be made finer, thereby significantly reducing the spheroidization heat treatment time. It relates to a method for producing a cold-rolled wire rod.
일반적으로 자동차, 산업기계 등의 부품 체결용으로 사용되는 볼트, 너트는 하기 표1에 나타난 성분의 중탄소강 선재를 소재로 사용하며, 그 제조공정은 강편을 선재압연하고, 신선, 구상화열처리, 냉간압조하는 일련의 공정을 통하여 제품화되고 있다.In general, bolts and nuts used for fastening parts of automobiles, industrial machines, etc. are used as materials of medium carbon steel wires as shown in Table 1 below, and the manufacturing process is rolled steel wires, drawing, spheroidizing heat treatment, cold It is commercialized through a series of processes for rolling.
상기 구상화열처리는 열간압연한 상태의 선재강도가 약 85㎏/㎟정도이고, 이러한 고강도강을 냉간에서 직접 압조하기가 곤란하기 때문에 압조가공전에 연화열처리를 실시한다. 구상화열처리는 통상 AC1변태온도 이상(약 750℃)에서 일정시간 유지하고 AC1이하의 일정온도(약 700℃)까지 서냉한 후 이 온도에서 일정시간 유지 후 냉각하고 있다. 이러한 열처리에 소요되는 시간은 약 15-20시간으로 열처리한 소재의 인장강도는 55㎏/㎟내외로 감소하게 된다. 소재가 이처럼 연화되는 이유는 열처리전의 페라이트 + 펄라이트 조직이 페라이트 + 구상시멘타이트로 변화되기 때문이다. 연화처리된 소재는 냉간압조 공정으로 옮겨서 볼트, 너트 형태로 냉간압조된다. 냉간압조는 특정 형태의 다이스(dies) 속에 소재를 삽입한 후 타격을 가하여 볼트 형상을 만드는 공정이다. 냉간압조공정에서는 변형이 된 부위에 균열이 발생하지 않아야 하며, 소재의 변형저항이 크지 않아야 한다. 이와 같은 냉간압조 가공을 통하여 제품화되는 종래소재의 경우, 강재의 연화를 위한 구상화소둔 열처리에 소요되는 시간이 너무 길고 또 소둔 온도가 높아서 생산성이 낮고, 제조비용이 높다는 것이다.In the spheroidizing heat treatment, the wire strength in the hot rolled state is about 85 kg / mm 2, and since it is difficult to directly press the high strength steel in cold operation, the softening heat treatment is performed before the rolling process. The spheroidizing heat treatment is usually maintained at a constant temperature above AC 1 transformation temperature (about 750 ° C.) for a predetermined time, and slowly cooled to a constant temperature below AC 1 (about 700 ° C.), and then cooled at a constant temperature at this temperature. The time required for such heat treatment is about 15-20 hours, the tensile strength of the heat treated material is reduced to about 55㎏ / ㎜. The reason for the softening of the material is that the ferrite + pearlite structure before heat treatment is changed to ferrite + spherical cementite. The softened material is transferred to the cold rolling process and cold pressed in the form of bolts and nuts. Cold pressing is a process of inserting a material into a specific type of die and then applying a blow to make a bolt shape. In the cold rolling process, there should be no crack in the deformed part and the deformation resistance of the material should not be large. In the case of the conventional material that is commercialized through such cold rolling process, the time required for the spheroidizing annealing heat treatment for softening the steel is too long and the annealing temperature is high, so that the productivity is low and the manufacturing cost is high.
이와같은 문제점을 해결하기 위하여 개발된 구상화 촉진강 선재 제조에 대한 공지된 기술내용을 살펴보면 다음과 같다. 먼저 미국 모르간(Morgan)사와 일본의 대동특수강사가 공동으로 개발한 새로운 압연설비를 이용하여 선재 마무리 압연온도를 700℃까지 낮추는 경우, 조직이 미세화되어 구상화열처리 시간을 종래재의 1/2 수준으로 단축할 수 있었다.Looking at the known technology for the manufacture of spheroidized steel rods developed to solve this problem is as follows. First, when the wire finish rolling temperature is lowered to 700 ° C by using a new rolling equipment jointly developed by Morgan and US Daedong Special Steel Co., the structure becomes finer and the spheroidization heat treatment time is reduced to 1/2 of conventional materials. Could.
또 다른 예는 일본 고배(KOBE)제철소에서는 20㎛이하로 미세하게 재결정된중탄소강의 오스테나이트를 850℃에서 마무리압연하여 압연재의 조직인 페라이트(Ferrite)와 펄라이트(Pearlite)조직을 미세화시킴으로써 구상화열처리 시간을 단축시켰다.Another example is spheroidization heat treatment by refined ferrite and pearlite structures of rolled material by finishing rolling austenite of medium-carbon steel recrystallized finely recrystallized to 20 μm or less at 850 ° C. in KOBE steel mill in Japan. Reduced time
상기 두가지 경우 공히 구상화촉진강을 제조하기 위해 압연온도를 850℃이하로 낮추어줌으로써 조직을 미세화시키고 있다. 그러나 압연온도를 낮추어주기 위해서는 압연기의 능력을 대폭 증강해 주어야하며, 또한 저온 압연재의 경우 선재의 단면형상이 불량하며, 선재를 권취하였을 때 코일(coil)의 권취형상이 불량해지는 문제점이 있다.In both cases, the structure is refined by lowering the rolling temperature below 850 ° C. in order to manufacture spheroidized steel. However, in order to lower the rolling temperature, the capability of the rolling mill should be greatly increased, and in the case of low-temperature rolling materials, the cross-sectional shape of the wire is poor, and the winding shape of the coil is poor when the wire is wound.
이에, 본 발명자들은 상술한 종래문제를 해결하기 위해 안출된 것으로써, 고온압연을 하더라도 조직을 미세화하여 구상화 열처리시간을 크게 단축할 수 있는 제조방법을 제공하는데, 그 목적이 있다.Accordingly, the present inventors have been made to solve the above-described conventional problem, to provide a manufacturing method that can significantly shorten the spheroidizing heat treatment time by miniaturizing the structure even when hot rolling.
도 1은 마무리압연온도에 따른 압연재의 미세조직을 나타내는 사진1 is a photograph showing the microstructure of the rolled material according to the finish rolling temperature
상기 목적을 달성하기 위한 본 발명은, 냉간압조용 선재의 제조방법에 있어서, 중량%로, C: 0.2-0.6%, Si: 0.1-1.0%, Mn: 0.3-1.5%, P: 0.03%이하, S: 0.05%이하, Al: 0.01-0.2%, Ti : 0.008-0.030%, N : 0.002-0.01% 및 잔부 Fe와 기타 불가피한 불순물로 이루어진 강편을 950-1200℃의 온도로 재가열한 후 900-1000℃의 마무리압연조건으로 열간선재압연한 다음, 5%이상의 가공량으로 신선한 후 740-780℃의 온도로 가열하여 1시간이상 유지하고, 이어 10-30℃/hr의 냉각속도로 690-710℃까지 냉각하여 1시간이상 유지한 후 통상의 방법대로 상온까지 냉각하는 것을 포함하여 구성된다.The present invention for achieving the above object, in the manufacturing method of the cold-rolled wire rod, by weight, C: 0.2-0.6%, Si: 0.1-1.0%, Mn: 0.3-1.5%, P: 0.03% or less , S: 0.05% or less, Al: 0.01-0.2%, Ti: 0.008-0.030%, N: 0.002-0.01%, and the steel slab consisting of the balance Fe and other unavoidable impurities after reheating to a temperature of 950-1200 ℃ 900- After hot-rolled at 1000 ℃ finish rolling condition, it is fresh with a processing amount of more than 5% and then heated to a temperature of 740-780 ℃ and maintained for more than 1 hour, followed by 690-710 at a cooling rate of 10-30 ℃ / hr. It is configured to include cooling to room temperature according to the usual method after cooling to ℃ and maintained for 1 hour or more.
이하, 본 발명에 대하여 상세히 설명한다.EMBODIMENT OF THE INVENTION Hereinafter, this invention is demonstrated in detail.
본 발명은 TiN석출물로 재결정된 오스테나이트의 성장을 효과적으로 억제시켜 고온압연을 하더라도 조직이 미세화되도록 함으로써, 구상화처리시간을 단축하는데, 그 특징이 있다.The present invention effectively suppresses the growth of austenite recrystallized with TiN precipitates, thereby making the structure finer even at high temperature rolling, thereby shortening the spheroidization treatment time.
이를위해 우선, 본 발명강의 성분중 상기, 탄소(C)는 첨가량이 0.2% 미만인 경우 강선재의 강도가 낮아서 구상화열처리를 실시할 필요가 없는 강종이므로 탄소량 0.2%미만에 대하여서 본 발명의 대상으로 하지 않는다. 첨가량이 0.6%이상이 되면 최종제품의 강도가 지나치게 높아지게 된다. 따라서 첨가범위를 0.2-0.6%로 제한하는 것이 바람직하다.To this end, among the components of the steel of the present invention, the carbon (C) is a steel that does not need to be subjected to spheroidizing heat treatment because the strength of the steel wire is low when the addition amount is less than 0.2%, the target of the present invention for less than 0.2% carbon content I never do that. If the added amount is more than 0.6%, the strength of the final product is too high. Therefore, it is desirable to limit the addition range to 0.2-0.6%.
상기 규소(Si)는 탈산효과 및 강도증가를 위해서 첨가하는데, 첨가량이 지나치게 적으면 이러한 효과를 얻기가 곤란하고 첨가량이 많으면 탈탄을 조장시켜 강재의 표면경도값 및 내구성을 감소시키므로 첨가범위를 0.1-1.0%로 한정하는 것이 바람직하다.The silicon (Si) is added to increase the deoxidation effect and strength, but when the addition amount is too small, it is difficult to obtain such an effect, and when the addition amount is large, it promotes decarburization to reduce the surface hardness value and durability of the steel, so that the addition range is 0.1-. It is preferable to limit to 1.0%.
상기 망간(Mn)은 강의 탈산에 필요한 원소이며 또한 소입성을 개선시킬 목적으로 첨가한다. 첨가량이 지나치게 적으면 이러한 효과를 얻기가 곤란하고, 첨가량이 많으면 강도가 지나치게 증가하고, 또 강선재 중심부에 경질의 마르텐사이트(Martensite) 조직이 발생되어 재질을 열화시키므로 첨가범위를 0.3-1.5%로 제한하는 것이 바람직하다.Manganese (Mn) is an element necessary for deoxidation of steel and is added for the purpose of improving hardenability. If the addition amount is too small, it is difficult to obtain such an effect. If the addition amount is too large, the strength is excessively increased, and a hard martensite structure is generated at the center of the steel wire, resulting in deterioration of the material. It is desirable to limit.
상기 인(P)은 0.03%이상 첨가되는 경우 소입소려시 균열발생을 조장하며 강의 인성을 떨어뜨리므로 0.03%이상 첨가되지 않도록 하여야 한다.When phosphorus (P) is added in an amount of 0.03% or more, cracking is promoted during quenching, and the toughness of steel is lowered, so it should not be added more than 0.03%.
상기 황(S)은 0.05%이상 첨가되는 경우 강의 충격인성을 감소시키므로 0.05%이상 첨가되지 않도록 하여야 한다.Sulfur (S) is to be added not less than 0.05% because it reduces the impact toughness of the steel when added more than 0.05%.
상기 알루미늄(Al)은 탈산 역할을 하며 또한 강중에서 질소(N) 와 반응하여 AlN을 형성하여 오스테나이트 입자성장을 억제하는 역할을 한다. 그러나 지나치게 많이 첨가하는 경우 알루미늄 산화물(Al2O3)를 형성하여 냉간압조성 및 충격인성을 떨어뜨린다. 따라서 알루미늄은 첨가범위를 0.01-0.2%로 제한하는 것이 바람직하다.The aluminum (Al) acts as a deoxidation and also reacts with nitrogen (N) in the steel to form AlN to inhibit austenite grain growth. However, when excessively added, aluminum oxide (Al 2 O 3 ) is formed to lower the cold pressure composition and impact toughness. Therefore, aluminum is preferably limited to the addition range of 0.01-0.2%.
상기 티타늄(Ti)은 강중에서 질소와 결합하여 질화티타늄(TiN)을 형성한다. 이러한 질화티타늄은 고온에서 안정하기 때문에 재결정된 오스테나이트의 성장을 효과적으로 억제시킨다. 그러나 첨가량이 지나치게 많으면 강중에 고용된 티타늄의 양이 증가하여 강재를 지나치게 강화시키고, 고가이므로 강재의 제조원가를 증가시키므로 첨가량을 0.008-0.03%로 한정하는 것이 바람직하다.The titanium (Ti) is combined with nitrogen in the steel to form titanium nitride (TiN). Since such titanium nitride is stable at high temperatures, it effectively suppresses the growth of recrystallized austenite. However, if the addition amount is too large, the amount of titanium dissolved in the steel is increased to excessively strengthen the steel, and because it is expensive, it is preferable to limit the addition amount to 0.008-0.03% because it increases the manufacturing cost of the steel.
상기 질소(N)는 앞에서 언급한 바와 같이 알루미늄, 티타늄과 결합하여 질화물을 형성하며 이것이 재결정된 오스테나이트의 성장을 억제시켜 조직을 효과적으로 미세화시킨다. 그러나 첨가량이 지나치게 많으면 고용 질소량이 증가하여 강재를 과도하게 강화시키므로 첨가량을 0.002-0.01%로 제한하는 것이 바람직하다.Nitrogen (N), as mentioned above, combines with aluminum and titanium to form nitride, which inhibits the growth of recrystallized austenite, thereby effectively miniaturizing tissue. However, if the amount added is too large, it is preferable to limit the amount added to 0.002-0.01% because the amount of solid solution nitrogen increases to excessively strengthen the steel.
상기와 같은 조성의 강을 강편으로 제조한 후 가열하여 선재압연을 실시하는데, 이때 가열온도는 950-1200℃범위로 하는 것이 바람직하다. 그 이유는 가열온도가 950℃이하가 되면 강의 변형저항이 너무커서 열간에서 선재로 압연하기가 곤란하며, 가열온도가 1200℃이상이 되면 탈탄이 심하게 발생하게 되어 최종 제품의 재질특성을 심하게 떨어드리며, 특히 오스테나이트 조직이 크게 성장하여 목표로 하는 미세한 조직을 얻기가 곤란해지기 때문이다.The steel having the composition described above is manufactured into steel pieces and then heated to perform wire rod rolling. In this case, the heating temperature is preferably in the range of 950-1200 ° C. The reason is that when the heating temperature is below 950 ℃, the deformation resistance of the steel is so great that it is difficult to roll it into the wire rod in the hot zone, and when the heating temperature is above 1200 ℃, decarburization occurs badly, which severely degrades the material properties of the final product. This is because, especially, austenite tissue grows significantly, making it difficult to obtain a target fine tissue.
상기와 같이 가열한 후 900-1000℃의 마무리압연온도 조건으로 열간압연하는 것이 바람직하다. 그 이유는 마무리압연온도가 900℃미만의 경우, 이상역에서 압연이 되므로 페라이트 조직이 경화되어 신성성이 떨어지고, 1000℃를 초과하는 경우 압연후 결정립이 크게 성장하므로 미세조직을 얻기가 곤란하기 때문이다.After heating as described above, it is preferable to perform hot rolling under the finishing rolling temperature condition of 900-1000 ° C. The reason is that when the finish rolling temperature is less than 900 ° C, the ferrite structure is hardened because the rolling is performed in the ideal region, and the stiffness is lowered. .
상기와 같은 조건으로 열간압연한 강재는 냉간압연 및 신선 등의 방법으로 냉간가공을 실시하는데, 냉간가공시 가공량은 5%이상으로 한다. 만일 이 보다 작은 가공도로 냉간가공을 실시하면 내부에너지 축적이 충분치 않고, 또 시멘타이트의 분절이 충분히 일어나지 않아서 구상화가 신속히 이루어지지 않는다.Steels hot-rolled under the above conditions are subjected to cold working by cold rolling and drawing, but the processing amount during cold working is 5% or more. If cold working is carried out with a smaller workability, internal energy accumulation is not sufficient, and cementite fragments do not sufficiently occur and spheroidization does not occur quickly.
상기와 같이 냉간가공을 마친 강재는 다시 740-780℃로 가열하여 1시간 이상 유지하고, 이어 10-30℃/hr의 속도로 690-710℃까지 냉각하고, 이 온도에서 1시간 유지한 후 통상의 방법대로 상온까지 냉각한다.The cold finished steel as described above is heated to 740-780 ℃ again and maintained for 1 hour or more, and then cooled to 690-710 ℃ at a rate of 10-30 ℃ / hr, and maintained at this temperature for 1 hour usually Cool to room temperature as instructed.
이러한 구상화열처리 조건에서 온도조건은 통상의 조건이며, 그 시간을 단축하는데 본 발명의 특징이 있다.In such spheroidizing heat treatment conditions, the temperature conditions are ordinary conditions, and the characteristics of the present invention are shortened in time.
상기 구상화열처리시 가열온도가 740℃이하가 되면, Ar1이하의 온도이기 때문에 세멘타이트가 분해되지 않는다. 따라서 740℃이하의 온도에서는 구상화에 걸리는 시간이 너무 길기 때문에 공업적으로 이용할 수가 없다. 가열온도를 780℃이상으로 하면 시멘타이트가 핵생성 될 수 있는 씨-드(seed)를 남기지 않고 모두 오스테나이트내로 재고용되기 때문에 냉각시 시멘타이트가 구상화되기 보다는 재생 펠라이트(Pearlite)가 생성된다.When the heating temperature is 740 ° C. or less during the spheroidizing heat treatment, the cementite is not decomposed because the temperature is less than or equal to Ar 1 . Therefore, at the temperature below 740 ° C, the time required for spheroidization is too long and cannot be used industrially. If the heating temperature is above 780 ° C, regenerated pelletite is produced rather than spheroidized when cementite is cooled because all of the cementite is re-used into austenite without leaving a seed that can nucleate.
가열시간을 1시간 이상으로 한정하는 이유는 시멘타이트의 분정 및 재고용을 위해 최소한 1시간 정도의 시간이 필요하기 때문이다.The reason for limiting the heating time to 1 hour or more is that at least one hour is required for the cementation and re-use of cementite.
가열 후 690-710℃까지 냉각할 때의 냉각속도를 한정하는 이유에 대하여 설명한다. 냉각속도가 10℃/hr이하가 되면 시멘타이트의 석출 및 성장할 수 있는 시간적인 여유가 없어서 구상화가 제대로 일어나지 않고, 냉각속도가 30℃/hr 이상이 되면 구상화 시멘타이트의 입자가 지나치게 조대해져서 재질을 열화시킨다.The reason for limiting the cooling rate at the time of cooling to 690-710 degreeC after heating is demonstrated. If the cooling rate is less than 10 ℃ / hr, there is no time for the precipitation and growth of cementite, the spheroidization does not occur properly. If the cooling rate is more than 30 ℃ / hr, the particles of spheroidized cementite become too coarse to deteriorate the material. .
냉각 목표온도를 690-710℃로 하는 이유는 710℃이상의 경우 변태구동력이 감소하여 구상화 속도가 느리게 진행되며, 690℃이하의 경우 탄소의 확산속도가 늦어져서 구상화 속도가 느려지기 때문이다.The reason why the cooling target temperature is 690-710 ° C. is because the transformation driving force decreases at 710 ° C. or higher, and the spheroidization rate is slowed down.
690-710℃에서 1시간 이상으로 유지하는 이유는 시멘타이트를 충분히 구상화시켜 강재를 냉간압조가공이 가능하도록 연화시키기 위함이다.The reason for maintaining at 690-710 ° C for more than 1 hour is to soften the steel to allow the cold rolling process by sufficiently spheroidizing cementite.
이어, 통상의 방법대로 상온까지 냉각하는데, 그 방법으로는 강선재를 약 660℃까지 시간당 약 20℃로 냉각시킨 후 공냉시키는 방법이 있다. 구상화 열처리가 끝난 선재는 필요한 선경으로 신선후 피막처리한 다음 냉각압조가공을 통하여 볼트로 가공한다.Subsequently, cooling to room temperature is carried out as usual, and the method includes cooling the steel wire to about 660 ° C. to about 20 ° C. per hour and then air-cooling it. The wire rod after spheroidization heat treatment is drawn to the required wire diameter and then coated and processed into bolts through cold press processing.
이하, 본 발명을 실시예를 통하여 보다 상세히 설명한다.Hereinafter, the present invention will be described in more detail with reference to Examples.
[실시예 1]Example 1
상기 표2와 같은 조성을 갖는 발명강과 종래강을 소형강괴(160mm x 160mm)로 제작한 다음 1200℃에서 2시간 가열하고, 마무리 압연온도를 900, 950℃, 1000℃로 변화시키면서 열간압연하였다.The invention steel and the conventional steel having the composition as shown in Table 2 were made of small ingots (160mm x 160mm) and then heated at 1200 ° C. for 2 hours, and hot-rolled while changing the finish rolling temperature to 900, 950 ° C. and 1000 ° C.
이때, 열간압연은 1150℃에서 30%의 압하율로 1차압연을 한 후 마무리압연온도에서 40%의 압하율로 마무리압연하고 이어 상온까지 1℃/sec 의 속도로 냉각한 다음 미세조직을 도 1에 나타내었다.At this time, hot rolling is performed by primary rolling at 30% reduction rate at 1150 ° C, and then finish rolling at 40% reduction rate at finishing rolling temperature, and then cooled to room temperature at a rate of 1 ° C / sec, and then microstructures are applied. 1 is shown.
도 1에 나타난 바와같이, 마무리 압연온도가 낮아질수록 미세조직이 미세해짐을 알 수 있었다. 그리고, 종래강보다 발명강의 미세조직이 훨씬 더 미세하였으므로, 종래강을 900℃마무리 압연하더라도 1000℃에서 마무리 압연한 발명강보다 더 조대하였다. 따라서, 본 발명강은 마무리압연온도를 높여도 종래강 대비 아주 미세한 조직을 확보할 수 있다는 것을 확인하였다.As shown in Figure 1, it can be seen that the microstructure becomes finer as the finishing rolling temperature is lowered. Further, since the microstructure of the invention steel was much finer than that of the conventional steel, even when the conventional steel was rolled at 900 ° C, it was coarser than the invention steel which was finish-rolled at 1000 ° C. Therefore, it was confirmed that the present invention steel can secure a very fine structure compared to the conventional steel even if the finishing rolling temperature is increased.
[실시예 2]Example 2
실시예 1에서 열간압연한 강재를 750℃에서 가열하여 1.5시간 유지한 후 20℃/hr의 냉각속도로 700℃까지 냉각하고, 이 온도에서 1.5시간 유지한 후 650℃까지 20℃/hr의 냉각속도로 서냉한 후 상온까지 공냉하여 구상화열처리한 다음, 경도를 측정하고 그 결과를 하기표 3에 나타내었다. 이때, 종래재의 경우 구상화열처리는 종래방법대로 15시간 열처리한 소재를 입수하여 경도값을 측정한 것이다.In Example 1, the hot-rolled steel was heated at 750 ° C. for 1.5 hours and then cooled to 700 ° C. at a cooling rate of 20 ° C./hr, and maintained at this temperature for 1.5 hours, then cooled to 20 ° C./hr up to 650 ° C. After cooling at slow rate and air-cooling to room temperature, spherical heat treatment was performed, and hardness was measured. The results are shown in Table 3 below. In this case, in the case of the conventional material, the spheroidization heat treatment is obtained by measuring the hardness value by obtaining the material heat-treated for 15 hours according to the conventional method.
상기 표3에 나타난 바와같이, 발명재(1-3)의 경우 종래재와 비교하여 구상화열처리시간을 거의 1/2로 단축하더라도 동등수준의 경도를 확보할 수 있었다.As shown in Table 3, the invention material (1-3) was able to secure the same level of hardness even if the spheroidizing heat treatment time is shortened to almost 1/2 compared with the conventional material.
이에 반해 종래강을 단시간(8시간) 구상화열처리한 비교재(1-3)의 경우 경도가 높아 장시간의 구상화 열처리가 필요하다는 것을 확인할 수 있었다.On the contrary, in the case of the comparative material (1-3) in which the conventional steel was spheroidized by heat treatment for a short time (8 hours), it was confirmed that the spherical heat treatment for a long time was necessary because of its high hardness.
결론적으로 티타늄과 질소가 소량 들어간 발명재(1-3)은 마무리압연온도를 900-1000℃로 하여도 구상화속도를 촉진할 수 있는 미세한 페라이트+펄라이트 조직을 얻을수 있었으며 구상화 속도도 굉장히 빨랐다. 따라서 본 발명에서 마무리 압연온도를 종래 공지기술과 같이 850℃이하로 내리지 않아도 구상화 촉진감을 제조할 수 있으므로, 저온압연을 위한 압연기 증강없이, 그리고 또 저온압연으로 인한 소재 단면 형상 불량 및 권취불량과 같은 문제점없이 구상화촉진이 가능한 감선재를 제조할 수 있다는 것을 확인하였다.In conclusion, the invention material (1-3) containing a small amount of titanium and nitrogen was able to obtain a fine ferrite + pearlite structure which can accelerate the spheroidization rate even at the finishing rolling temperature of 900-1000 ° C. Therefore, in the present invention, it is possible to produce a spheroidization feeling without lowering the finishing rolling temperature below 850 ° C as in the prior art. It was confirmed that a wire-sensitive material capable of spheroidizing promotion could be produced without problems.
상술한 바와같이, 본 발명은 강중 티타늄과 질소함량을 적절히 첨가하여 강 조성을 제어하는 한편 열간압연을 적절히 수행함으로써, 구상화시간을 대폭 단축시킬 수 있다. 따라서 열처리 비용을 크기 줄일 수 있고, 생산공정이 짧아져서 납기단축 및 생산성 향상 등의 효과가 있는 것이다.As described above, the present invention can significantly reduce the spheroidization time by appropriately adding titanium and nitrogen content in steel to control the steel composition and performing hot rolling appropriately. Therefore, the heat treatment cost can be reduced in size, and the production process is shortened, thereby reducing the delivery time and improving productivity.
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CN102994710B (en) * | 2012-12-28 | 2014-11-26 | 东莞市科力钢铁线材有限公司 | Spheroidizing annealing process of superplasticity fastener wire rod |
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