WO2011139117A2 - 초미세립 고강도 고인성 선재 및 그 제조방법 - Google Patents
초미세립 고강도 고인성 선재 및 그 제조방법 Download PDFInfo
- Publication number
- WO2011139117A2 WO2011139117A2 PCT/KR2011/003396 KR2011003396W WO2011139117A2 WO 2011139117 A2 WO2011139117 A2 WO 2011139117A2 KR 2011003396 W KR2011003396 W KR 2011003396W WO 2011139117 A2 WO2011139117 A2 WO 2011139117A2
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- strength
- wire rod
- ferrite
- wire
- ultrafine
- Prior art date
Links
Classifications
-
- 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
-
- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/003—Cementite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
Definitions
- the present invention relates to a high-strength high toughness wire, and more particularly, to a wire rod having excellent strength and toughness and a method of manufacturing the same by controlling the microstructure.
- the grain size of the ferrite crystal grains can be reduced to about 20.
- TMCP Thermo Mechanical Control Process
- all of the above-mentioned particle refining techniques are techniques that can be used in the production of plate materials, and are difficult to apply to wire rods. That is, compared with thick steel, wire rods have a much higher cross-sectional reduction rate, so the rolling speed is very fast, and it is not easy to control the angular speed.
- martensite is formed on the surface, which may cause surface defects.
- Patent relates to a technique for producing a high strength high toughness of the wire rod, the fine granules may, etc.
- the segmented cementite acts as a fine precipitated curable material, and has the advantage of dramatically increasing the strength of the wire rod, but according to the Hall-Petch relation, the strength increases.
- the disadvantage is that it inevitably involves a decrease in ductility.
- rolling should be performed after cementite has already been produced. Therefore, it is necessary to widen the two-phase region where cementite can be produced.
- Other fine grain wires include ultra fine grain wires using powder metallurgy using fine powders.
- wire wires from powder metallurgy are limited in their use. The situation has not been overcome.
- the number of techniques for manufacturing ultrafine grained wire rods by other rolling or engraving methods is very limited in number, and most of them are merely a technique of limiting the size of pearlite structure by controlling finish rolling and LP lead patenting temperature.
- these techniques are hardly seen as having a special technical meaning. Therefore, the technology for manufacturing ultrafine grained wire rod using carbon steel has high utility value but has not yet been presented with satisfactory technology. Accordingly, there is an urgent need for technology development.
- a wire rod having a high strength and high toughness and a method of manufacturing the same are provided.
- the wire rod has a microstructure including a ferrite structure of 60% or more by area fraction, the remainder of cementite structure,
- the ferrite has an average particle diameter of 15 m or less to provide an ultrafine grain high strength high toughness wire.
- the wire rod rolled wire 150 It provides a method for producing ultrafine high-strength, high-strength wire rod comprising a rapid angle down to -100 ° C, after the angle to ⁇ 350 ° C.
- an ultrafine, high-strength, high toughness wire rod that can secure the tensile strength and elongation of the alloy steel level using carbon steel without the alloying elements.
- FIG. 1 are photographs of the microstructures of Comparative Example 1 and Inventive Example 1 of steel grade 1 in Example 1, respectively.
- Figure 2 is a graph showing the results of measuring the tensile strength of Comparative Examples and Inventive Examples of Steel Grades 1 and 2 in Example 1.
- Figure 3 (a) is the result of EBSD image of Example 2 of steel grade 2 in Example 1, (b) is a photograph observing the microstructure.
- 4 (a) and 4 (b) are graphs showing mechanical properties after drawing and annealing the wire rods of Comparative Example 2 and Inventive Example 2 of steel grade 2 in Example 2, respectively.
- the present inventors studied a method for producing a high strength, high toughness wire without using a ferroalloy containing expensive alloying elements such as Ti, Nb, and V with respect to the carbon steel wire.
- the present inventors have developed a wire rod having a microstructure of wire rod as an area fraction, 60% or more of ferrite tissue, and the remainder including cementite tissue, and the average particle diameter of the ferrite is 15 or less. It has now been realized that high toughness can be achieved and the present invention has been reached.
- the microstructure satisfies 60% or more of ferrite in an area fraction, and the rest includes cementite.
- the fraction of the ferrite is less than 60%, due to the decrease of the ferrite fraction, the ductility is lowered, there is a problem that the balance of strength and toughness is lowered by the Hall-Petch equation according to the improvement of strength
- the fraction preferably satisfies 60% or more.
- the average particle diameter of the ferrite of the wire rod of the present invention satisfies the following. As described above, when the size of the crystal grains of the ferrite decreases, the specific surface area of the crystal grains increases, so that a smooth slip system works and the strength increases, but the ductility does not decrease.
- the wire rod of the present invention can secure a ductility having a high elongation while maintaining a high tensile strength. If the average particle diameter of the ferrite is greater than 15 / zm and the ferrite grain size is not reduced, the strength increase effect is insignificant, and the ferrite fraction per unit area decreases, thereby reducing the toughness and ductility. There is a problem that it is difficult to secure an increase effect.
- the ferrite preferably has the shape of bainite. This shape of ferrite is called bainitic ferrite.
- the bainitic ferrite has a needle-like shape and is composed of a lath-like tissue.
- the bainitic ferrite is free of internal precipitates and is composed of parallel lath groups having a parental austenite and a specific habit plane. Since these lath groups all have the same variation, the orientation difference between them is extremely small, thereby forming the small-angle grain boundary described later.
- the wire rod of the present invention includes the bainitic ferrite, and has an effect of increasing the toughness, ductility, and strength at the same time by increasing the ferrite fraction compared to the general ferrite.
- the crystal orientation of the Electro Back Scattered Diffract ion (EBSD) is preferably 30 ⁇ or less. The crystal orientation is
- the wire rod of the present invention forms a small grain angle grain boundary to increase the fine ferrite fraction and not only improve the strength, but also increase the toughness and ductility, thereby forming a structure capable of improving mechanical properties.
- the wire composition of the present invention is that the content of carbon (C) is 0.15 to 0.5% by weight, 0.1 0.2% by weight of silicon (Si) and 0.1-0.7% by weight of manganese (Mn). desirable.
- the rest includes Fe and unavoidable impurities.
- other components may be added, but the addition of other components does not affect the technical spirit of the present invention.
- the wire rod of the present invention has a tensile strength of llOOMpa or more, an elongation of 20% or more, and an echo (EC0) index (tensile strength X elongation), which represents a strength and ductility, of 2000 or more.
- EC0 echo index
- tensile strength X elongation which represents a strength and ductility, of 2000 or more.
- wire rods are produced by heating a bloom or billet, rolling the wire rod, followed by engraving and winding.
- a process for producing the carbon steel wire after reheating the carbon steel bloom or billet to 1100 o C or more,
- the wire is rolled in the temperature range of 1000 ⁇ 900 ° C, and manufactured by winding after stamping.
- the wire rod manufacturing method of the present invention when manufacturing the wire rod, the wire rod is rolled
- the process of engraving the wire rod to 150 ⁇ 350 ° C is preferably carried out by a common process.
- the rapid angle does not mean normal water cooling or cooling, but means rapid angle in seconds. This is generally recognized as having a martensite structure when quenching the heated steel, but the present invention is to escape this conventional concept.
- by performing the rapid tilting it is possible to suppress the diffusion in the process of tilting to suppress the grain growth, and after rolling by the rapid tilting, the state just before the microstructure is recrystallized, that is, the seed like in the tissue (such as bainite structure) Grain freezing takes place, forming sheaf-like laths.
- a microstructure composed of ferrite and cementite having fine grains is formed.
- the ferrite grain is grown micro-forming the fine granules of the tissue, are typically "transformation is suppressed that occurs in the steel, more than 60% ferrite and the rest of the cementite tissue To form.
- the ferrite is formed of bainitetic ferrite.
- the preferred angle of incidence of the rapid angle is 100-150 ° C./sec.
- the rapid angle does not mean normal water, but is to use the freezing of the grains through the following sales, the angle of angular velocity should be 100 o C / sec or more, preferably Carry out at an angular velocity of 100 to 150 ° C / sec.
- a solvent used for the rapid wetting liquid nitrogen, dry ice, or the like may be used, or a polymer solution for wire wetting may be used. Preferred examples of such polymer solutions consist of 15-30% polyalkylene glycol (PAG) and 70-85% water (0).
- the most preferable example of the solvent is liquid nitrogen. Is to the rapid nyaenggak is nyaenggak the wire to a temperature range of not more than -ioo o C, and preferably -
- the rapid angle is preferably immersed in a solvent, and the time of immersion is preferably 1 to 10 minutes. If the time is less than 1 minute, the cooling of the wire rod does not become a layer, the structure required by the present invention cannot be formed, and if the time becomes too long for more than 10 minutes, the time in the wire rod manufacturing process becomes too long and the productivity is increased. May result in deterioration.
- FIGS. 1 and 3 are photographs of the microstructures of Comparative Example 1 and Inventive Example 1 of the steel grade 1, respectively.
- Comparative Example 1 can be seen that consists of two phases of about 35-40 ferrite and cementite, but in the case of Inventive Example 1 shown in Figure 1 (b) It can be seen that it is composed of ultrafine ferrite (bainitic ferrite) and cementite formed like bainite of /.
- Figure 2 is a graph showing the results of measuring the tensile strength of the comparative examples and invention examples of the steel grades 1 and 2.
- Tensile Strength (Tensile Strength) in the steel grades 1 and 2 it can be seen that the invention strengths of about 1.5 times to 2 times the tensile strength compared to the comparative examples.
- FIG. 3 (a) is a photograph showing the EBSD (Electro Back Scattered Diffraction) image of Example 2 of steel grade 2
- Figure 3 (b) is a photograph showing the microstructure of Example 2 of the steel grade 2.
- Inventive Example 2 shows that a small-angle grain boundary having a crystal orientation of 30 ° or less is formed, as shown in (b) of FIG. 3.
- the crystal grains of ferrite are about 12 / tong or less.
- Example 2 was performed as follows. A dry fresh specimen of Comparative Example 2 of the steel grade 2 up to 80%, and a specimen annealed to 500 ° C, 600 ° C, respectively, to prepare a specimen, dry fresh fresh to 80% of Example 2 of the steel grade 2 Ash was prepared. Their mechanical properties were measured and the results are shown in FIG. 4.
- Figure 4 (a) is a dry fresh specimen of Comparative Example 2, showing the mechanical properties of the annealed wire material, (b) shows a dry fresh wire material of Example 2 at the same time.
- the tensile strength may be increased to about 1600 MPa, but according to a typical Hall-Patch effect. It can be seen that this indicates less than about 10%, and the ductility did not increase even after the annealing performed for loosening the dense dislocations.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Crystallography & Structural Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Manufacturing & Machinery (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
- Metal Extraction Processes (AREA)
Abstract
Description
Claims
Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CN201180022757.5A CN102884211B (zh) | 2010-05-06 | 2011-05-06 | 高强度和高韧性超细线材及其生产方法 |
US13/695,121 US9322075B2 (en) | 2010-05-06 | 2011-05-06 | High-strength and high-toughness ultrafine wire rod |
EP11777598.1A EP2568056B1 (en) | 2010-05-06 | 2011-05-06 | High-strength and high-toughness ultrafine wire rod and method for producing same |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
KR10-2010-0042498 | 2010-05-06 | ||
KR1020100042498A KR101253822B1 (ko) | 2010-05-06 | 2010-05-06 | 초미세립 고강도 고인성 선재 및 그 제조방법 |
Publications (2)
Publication Number | Publication Date |
---|---|
WO2011139117A2 true WO2011139117A2 (ko) | 2011-11-10 |
WO2011139117A3 WO2011139117A3 (ko) | 2012-05-18 |
Family
ID=44904244
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/KR2011/003396 WO2011139117A2 (ko) | 2010-05-06 | 2011-05-06 | 초미세립 고강도 고인성 선재 및 그 제조방법 |
Country Status (5)
Country | Link |
---|---|
US (1) | US9322075B2 (ko) |
EP (1) | EP2568056B1 (ko) |
KR (1) | KR101253822B1 (ko) |
CN (1) | CN102884211B (ko) |
WO (1) | WO2011139117A2 (ko) |
Families Citing this family (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2014171427A1 (ja) * | 2013-04-15 | 2014-10-23 | 新日鐵住金株式会社 | 熱延鋼板 |
CN103422024B (zh) * | 2013-05-15 | 2015-10-07 | 锡山区羊尖泓之盛五金厂 | 一种铬锰氮合金及其制备方法 |
CN108396246B (zh) * | 2017-02-08 | 2020-09-01 | 鞍钢股份有限公司 | 一种高碳钢盘条及其网状渗碳体析出控制方法 |
CN113186438B (zh) * | 2021-01-20 | 2022-09-13 | 厦门虹鹭钨钼工业有限公司 | 一种合金线材及其制备方法与应用 |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2009062574A (ja) | 2007-09-05 | 2009-03-26 | Kobe Steel Ltd | 伸線加工性に優れた線材およびその製造方法 |
JP2009132958A (ja) | 2007-11-29 | 2009-06-18 | Nippon Steel Corp | 鋼線材のインライン熱処理方法およびその装置 |
JP2009138251A (ja) | 2007-12-10 | 2009-06-25 | Kobe Steel Ltd | 伸線性に優れた鋼線材 |
Family Cites Families (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH084837B2 (ja) | 1987-12-28 | 1996-01-24 | 三菱マテリアル株式会社 | 極細線の製造方法 |
US20060057419A1 (en) * | 2003-01-17 | 2006-03-16 | Toru Hayashi | High-strength steel product excelling in fatigue strength and process for producing the same |
CA2528165A1 (en) * | 2003-06-05 | 2004-12-16 | Questek Innovations Llc | Nano-precipitation strengthened ultra-high strength corrosion resistant structural steels |
JP2009144230A (ja) | 2007-12-18 | 2009-07-02 | Nakayama Steel Works Ltd | 鋼線材およびボルト、ならびに鋼線材の製造方法 |
KR101008112B1 (ko) * | 2008-10-24 | 2011-01-13 | 주식회사 포스코 | 선재 냉각용 폴리머 솔루션 및 그 제조방법과 상기 폴리머 솔루션을 이용한 냉각방법 및 그 냉각방법에 의해 제조된 선재 |
KR101125958B1 (ko) * | 2009-06-12 | 2012-03-21 | 주식회사 포스코 | 가변열처리장치 및 이를 이용한 고강도 고연성 신선재의 제조방법 |
-
2010
- 2010-05-06 KR KR1020100042498A patent/KR101253822B1/ko active IP Right Grant
-
2011
- 2011-05-06 CN CN201180022757.5A patent/CN102884211B/zh not_active Expired - Fee Related
- 2011-05-06 US US13/695,121 patent/US9322075B2/en active Active
- 2011-05-06 WO PCT/KR2011/003396 patent/WO2011139117A2/ko active Application Filing
- 2011-05-06 EP EP11777598.1A patent/EP2568056B1/en not_active Not-in-force
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2009062574A (ja) | 2007-09-05 | 2009-03-26 | Kobe Steel Ltd | 伸線加工性に優れた線材およびその製造方法 |
JP2009132958A (ja) | 2007-11-29 | 2009-06-18 | Nippon Steel Corp | 鋼線材のインライン熱処理方法およびその装置 |
JP2009138251A (ja) | 2007-12-10 | 2009-06-25 | Kobe Steel Ltd | 伸線性に優れた鋼線材 |
Non-Patent Citations (1)
Title |
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See also references of EP2568056A4 |
Also Published As
Publication number | Publication date |
---|---|
US20130048159A1 (en) | 2013-02-28 |
KR20110123066A (ko) | 2011-11-14 |
CN102884211A (zh) | 2013-01-16 |
KR101253822B1 (ko) | 2013-04-12 |
EP2568056B1 (en) | 2016-11-30 |
WO2011139117A3 (ko) | 2012-05-18 |
CN102884211B (zh) | 2016-06-08 |
EP2568056A4 (en) | 2015-07-08 |
US9322075B2 (en) | 2016-04-26 |
EP2568056A2 (en) | 2013-03-13 |
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