EP2682489B1 - High-carbon steel wire rod excellent in drawability and fatigue characteristics after wire drawing - Google Patents

High-carbon steel wire rod excellent in drawability and fatigue characteristics after wire drawing Download PDF

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Publication number
EP2682489B1
EP2682489B1 EP12751796.9A EP12751796A EP2682489B1 EP 2682489 B1 EP2682489 B1 EP 2682489B1 EP 12751796 A EP12751796 A EP 12751796A EP 2682489 B1 EP2682489 B1 EP 2682489B1
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inclusions
steel
wire rod
drawability
composition
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English (en)
French (fr)
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EP2682489A1 (en
EP2682489A4 (en
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Hajime Hasegawa
Wataru Yamada
Akihito Kiyose
Kouichi Kudou
Shingo Yamasaki
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Nippon Steel Corp
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Nippon Steel Corp
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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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C1/00—Manufacture of metal sheets, metal wire, metal rods, metal tubes by drawing
    • B21C1/003—Drawing materials of special alloys so far as the composition of the alloy requires or permits special drawing methods or sequences
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/04—Removing impurities by adding a treating agent
    • C21C7/06—Deoxidising, e.g. killing
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
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    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron

Definitions

  • the present invention relates to wire rod for drawing purposes, in particular high carbon steel wire rod and wire rod for valve springs which are excellent in drawability and fatigue characteristics after drawing.
  • the wire of the present invention is used, after drawing, for example, for steel cord for automobile tires, saw wire for cutting silicon for solar cells or semiconductors, valve springs for automobile engines, long rubber belts, aircraft tires, bridge ropes, etc.
  • high carbon steel wire rod which is used for drawing purposes has to be able to be drawn at a high speed and has to be excellent in fatigue resistance after drawing.
  • hard oxide-based nonmetallic inclusions may be mentioned.
  • oxide-based inclusions inclusions of Al 2 O 3 , SiO 2 , CaO, TiO 2 , MgO, and other single-composition or binary systems of MgO ⁇ Al 2 O 3 or 2MgO ⁇ SiO 2 are high in hardness and nonviscous. Therefore, to produce high carbon steel wire rod excellent in drawability, it is necessary to raise the cleanliness of the molten steel and soften the oxide-based inclusions.
  • PLT 1 shows a method of production of steel for high carbon steel excellent in drawability.
  • PLT 2 discloses a method of production of extremely fine wire. The basic idea of these arts is limited to three-component system oxide-based nonmetallic inclusions of Al 2 O 3 -SiO 2 -MnO.
  • PLT 3 proposes making nonmetallic inclusions the Spessartite region in a Al 2 O 3 , SiO 2 , MnO three-component phase diagram so as to improve the drawability of the product.
  • PLT 4 discloses a method of restricting the amount of Al which is added to the molten steel so as to reduce harmful inclusions and improve the drawability.
  • PLT 5 relates to production of steel cords of a nonviscous inclusion index of 20 or less and proposes to blow CaO-containing flux together with a carrier gas (inert gas) into the ladle molten steel while completely restricting Al so as to perform preliminary deoxidation, then blow in an alloy which contains one or more of Ca, Mg, and REM and thereby soften the inclusions.
  • a carrier gas inert gas
  • PLT 6 restricts the range of the total oxygen content to a certain range to control the amount and composition of the nonviscous inclusions, reduces the size and number of nonviscous inclusions and secures ductility to thereby make the amount and distribution of size of nonviscous inclusions the preferable state, further, adds the composition of inclusions to SiO 2 and MnO, and reforms them to multi-component oxide-based inclusions which selectively contain Al 2 O 3 , MgO, CaO, and TiO 2 so as to soften the inclusions and realize high carbon steel wire rod extremely excellent in drawability and fatigue resistance after drawing.
  • PLT 7 discloses the method of limiting the sizes of hard high SiO 2 inclusions and reducing the amount of use of expensive deoxidizing alloys.
  • PLT 8 proposes to use a mixture of an Si-based deoxidizing agent and an alkali metal compound so as to control the amount of alkali metal compound in the nonmetallic inclusions to 4 to 24% and improve the stretchability.
  • PLT 9 proposes Si-killed steel which is excellent in fatigue strength characterized by including 0.5 to 10% of an oxide of an alkali metal in Al 2 O 3 -CaO-SiO 2 -MgO-MnO-based low melting point inclusions.
  • PLTs 10 and 11 disclose steel wire for high cleanliness springs excellent in fatigue characteristics characterized by including one or more of LiO 2 , Na 2 O, and K 2 O in a total of LiO 2 , Na 2 O, and K 2 O of 0.5 to 20% in low melting point inclusions. These describe that LiO 2 , Na 2 O, and K 2 O are not equal and that by positively adding Li with its particularly strong deoxidizing power as the source of formation of the oxide-based inclusions, the effect is raised if including a suitable amount of LiO 2 in the oxide-based inclusions.
  • NPLT 1 Iron and Steel Institute of Japan ed. Third Edition Iron and Steel Handbook, II. Iron-making and Steel-making, page 690
  • the present invention was made in consideration of the above situation and has as its topic the supply of high performance high carbon wire rod which is able to handle even tough applications, which is extremely low in wire breakage rate at the time of drawing, and which is excellent in fatigue characteristics after wire drawing by utilizing the basic technique of multi-component control of oxide-based nonmetallic inclusions and utilizing compounds other than oxides so as to cause a distinctive drop in the melting point and viscosity of nonmetallic inclusions and refine the inclusions after wire rod rolling.
  • the inventors investigated in detail the relationship between the composition of nonmetallic inclusions and the melting point or viscosity. As a result, they discovered that by establishing the copresence of Na or another alkali metal and a fine amount of fluorine in multi-component inclusions, it is possible to further lower the melting point and viscosity of inclusions, possible to control the formation of the crystal phases, and as a result possible to refine the inclusions after wire rod rolling.
  • the conventional technique for multi-component control of nonmetallic inclusions was a technique lowering the melting point and viscosity of silicate inclusions.
  • Na and F are extremely strong in affinity. Seen from a micro viewpoint, Na ions and F ions are positioned close by and influence the melting point and viscosity of silicate inclusions as NaF molecules.
  • Oxides containing NaF start to melt at a temperature of 1200°C or less, while oxides to which only Na 2 O is added and oxides to which only F (for example, CaF 2 ) is added do not start melting until a high temperature of over 1200°C. That is, by establishing the copresence of Na and F, an extremely low melting point can be realized.
  • This melting point of 1200°C or less is a temperature close to not only the blooming in the breakdown process of a continuously cast steel slab (1150 to 1300°C), but also to the wire rod rolling temperature (1000 to 1200°C).
  • the stretching of inclusions at the time of rolling occurred mainly in the blooming process.
  • Na and F are copresent in inclusions
  • the inclusions are stretched not only in the blooming process, but also in the wire rod rolling process. Therefore, by establishing the copresence of Na and F, it is possible to refine inclusions much more.
  • the effect of Na and F on the stretchability of inclusions depends on the calculated amount of NaF in the inclusions. If the calculated amount of NaF increases, the stretchability is improved.
  • the "calculated amount of NaF” means the mass% of NaF in the inclusions when Na and F are bonded 1:1 in molar ratio.
  • PLTs 8 to 11 disclose methods using oxides of alkali metals such as Na.
  • alkali metals such as Na.
  • the reasons for limitation of the total oxygen amount in the steel will be explained.
  • the amount of nonmetallic inclusions becomes greater and wire breakage cannot be sufficiently avoided in worked materials used for tough applications, so the upper limit is made 30 ppm.
  • a total oxygen content of 16 ppm or more is necessary. If the total oxygen amount is less than 16 ppm or more than 30 ppm, the die life becomes extremely poor.
  • the more preferable range of the total oxygen amount is 17 to 25 ppm.
  • Inclusions with a short axis of less than 0.5 ⁇ m in the wire rod L cross-section are inclusions which are inherently small in size or which easily deform during rolling.
  • Inclusions with a long axis of less than 1.0 ⁇ m and a circle equivalent diameter of less than 1.0 ⁇ m are inclusions which are inherently small in size. These inclusions tend to not become causes of deterioration of the drawability and fatigue characteristics.
  • oxide-based nonmetallic inclusions with a short axis of 0.5 ⁇ m or more, a long axis of 1.0 ⁇ m or more, and a circle equivalent diameter of 1 ⁇ m or more, seen in the cross-section of a wire rod, were defined as inclusions for evaluation and are called "inclusions covered due to size".
  • the oxide composition is based on a five-component system of SiO 2 -CaO-Al 2 O 3 -MgO-MnO. Na and F are simultaneously included whereby for the first time the effects of softening and refining the nonmetallic inclusions are exhibited.
  • SiO 2 is an important oxide forming the basis of the silicate inclusions. If (%SiO 2 ) is less than 40%, the base multi-component inclusions themselves will not become silicate inclusions and the effects of the present invention cannot be exhibited. If (%SiO 2 ) exceeds 95%, the result no longer becomes multi-component inclusions and large sized SiO 2 causes deterioration of quality.
  • (%CaO) has to be made 0.5% or more to obtain the effect of reduction of the melting point and viscosity by formation of multi-component inclusions. If (%CaO) exceeds 30%, CaO-rich hard inclusions are formed and a deterioration of quality occurs.
  • Al 2 O 3 contributes to softening of inclusions if in a suitable quantity, but if exceeding 30% as (%Al 2 O 3 ), hard Al 2 O 3 inclusions are formed and the quality greatly deteriorates. If (%Al 2 O 3 ) is less than 0.5%, the effect of the multi-component inclusions is not obtained.
  • (%MgO) has to be made 0.5% or more to obtain the effect of reduction of the melting point and viscosity by formation of multi-component inclusions. If (%MgO) exceeds 20%, olivine or foresterite (2MgO ⁇ SiO 2 ) or other harmful inclusions are formed.
  • (%MnO) has to be made 0.5% or more to obtain the effect of reduction of the melting point and viscosity by formation of multi-component inclusions. If (%MnO) exceeds 10%, the inclusions become not silicate inclusions, but Spessartite (SiO 2 -MnO-Al 2 O 3 ) inclusions and the effects of addition of Na and F are no longer exhibited.
  • Na and F are extremely important ingredients in the present invention. If (%Na) is less than 0.2%, there is no effect of improvement of stretchability of inclusions. On the other hand, if (%Na) is over 7%, the problems arise that the effect becomes saturated and the amount of dust generated when adding Na rapidly rises.
  • the content is preferably less than 4%.
  • (%F) is less than 0.17%, there is no effect of improvement of stretchability of inclusions. If (%F) is over 8%, the effect becomes saturated and problems such as a rapid increase in the refractory melt loss become greater.
  • Na and F exhibit their effects after forming NaF molecules in the inclusions, so they are preferably added so that the molar ratio of Na and F in the nonmetallic inclusions becomes 1:1, that is, by mass ratio, (%Na):(%F) become close to 1:0.83.
  • the number ratio falling under 80% means that the effect of stretching of inclusions by Na+F cannot be enjoyed. Further, falling under 80% means, for example, the presence of a certain amount of inclusions of compositions not belonging to multi-component inclusions such as MgO-based or Al 2 O 3 -based hard inclusions. As a result, the drawability and the fatigue characteristics after wire drawing are impaired.
  • the reason for defining the size of the inclusions is to count only inclusions of a size causing deterioration of the drawability and fatigue characteristics.
  • both Na and F into the steel include both Na and F in the silicate-based multi-component oxide-based inclusions, and control the composition of inclusions so as to secure excellent drawability and fatigue characteristics after wire drawing.
  • applications are increasing in which the steel wire rods are drawn more finely. In such applications, the high carbon steel wire rods of the present invention exhibit particularly excellent performance.
  • the method of addition of Na and F may be to add them as an NaF compound. It is also possible to add Na and F separately (for example, Na 2 CO 3 and CaF 2 etc.)
  • REM La, Ce, Nd, etc.
  • S fixes S in the form of REM oxysulfide (REM 2 O 2 S), and is taken into the multi-component inclusions. Due to this, it is possible to reduce the amount solid solution S in the steel and precipitation of MnS is suppressed.
  • MnS which is precipitated in the steel sometimes becomes the starting point of breakage during drawing. By suppressing this precipitation, the drawability and the fatigue characteristics after wire drawing are improved.
  • the (%T.REM) of the inclusions covered due to composition should be controlled to 0.3 to 1.0%, while (%S) should be controlled to 0.05 to 0.2% in range. If (%T.REM) is less than 0.3%, the S fixing ability is insufficient, while if over 1.0%, the concentration of REM oxides in the nonmetallic inclusions increases and the stretchability is sometimes not sufficiently improved. Further, if (%S) is less than 0.05%, the fixed amount of S is too small and there is no effect, while if over 0.2%, CaS etc. is formed in the nonmetallic inclusions and the stretchability is sometimes not sufficiently improved.
  • wire breakage starting from MnS is less frequent compared with wire breakage starting from oxide-based nonmetallic inclusions. Therefore, first, it is necessary to suitably control the composition of oxide-based nonmetallic inclusions in the steel.
  • killed steel is used for wire which is used as high carbon steel wire rod such as_the piano wire of JISG3502, hard steel wire rod of JISG3506, and oil tempered wire for valve springs of JISG3561.
  • high carbon steel wire rod such as_the piano wire of JISG3502, hard steel wire rod of JISG3506, and oil tempered wire for valve springs of JISG3561.
  • the steel is steel which consists of , by mass%, C: 0.5 to 1.2%, Si: 0.15 to 2.5%, Mn: 0.20 to 0.9%, P ⁇ 0.025%, S: 0.004 to 0.025%, Al: 0.000005 to 0.002%, Ca: 0.00001 to 0.002%, Mg: 0.00001 to 0.001%, Na: 0.000005 to 0.001%, and F: 0.000005 to 0.001% and which contains, in accordance with need, one or more types of Cr: 0.05 to 1.0%, Ni: 0.05 to 1.0%, Cu: 0.05 to 1.0%, Ti: 0.001 to 0.25%, V: 0.001 to 0.25%, Nb: 0.001 to 0.25%, Mo: 0.05 to 1.0%, and Co: 0.1 to 2%.
  • C is an element which is economic and effective in strengthening the steel. To obtain the strength required as a hard steel wire, 0.5% or more is necessary. However, if over 1.2%, the steel falls in ductility and becomes brittle and secondary working becomes difficult, so the content is made 1.2% or less. The more preferable concentration of C is 0.51 to 1.1%.
  • Si and Mn are required for deoxidation and control of the composition of inclusions. If Si is less than 0.15% and Mn is less than 0.20%, there is no effect. Further, while also effective as a steel strengthening element, if Si is over 2.5% and Mn is over 0.9%, the steel becomes brittle.
  • the more preferable ranges of Si and Mn are respectively 0.16 to 2.3% and 0.25 to 0.85%.
  • the content of P causes degradation of the wire drawability in high carbon steel and further causes degradation of the ductility after wire drawing. Accordingly, the content of P has to be made 0.025% or less, more preferably is 0.020% or less.
  • S also causes degradation of the wire drawability and further causes degradation of the ductility after wire drawing.
  • the content of S is 0.004 to 0.025%, preferably 0.005 to 0.020%.
  • A1 is an element which influences the composition of inclusion of the present invention. If too great or too small, a predetermined composition of inclusions cannot be obtained. Accordingly, the concentration of Al is 0.000005 to 0.002%, preferably 0.0002 to 0.001%.
  • Ca is also an element which influences the composition of inclusions of the present invention. If too great or too small, a predetermined composition of inclusions cannot be obtained. Accordingly, the concentration of Ca is made 0.00001 to 0.002%, preferably 0.000013 to 0.0015%.
  • Mg also is an element which influences the composition of inclusions of the present invention, If too great or too small, a predetermined composition of inclusions cannot be obtained. Accordingly, the concentration of Mg is made 0.00001 to 0.001%, preferably 0.000011 to 00008%.
  • Na and F are extremely important ingredients in the composition of inclusions of the present invention.
  • concentrations of Na and F in the steel influences the composition of inclusions.
  • Na is an element which influences the composition of inclusions of the present invention. If too great or too small, a predetermined composition of inclusions cannot be obtained. Accordingly, the concentration of Na is made 0.000005 to 0.001%, preferably 0.000007 to 0.0005%.
  • F is also an element which influences the composition of inclusions of the present invention. If too great or too small, a predetermined composition of inclusions cannot be obtained. Accordingly, the concentration of F is made 0.000005 to 0.001%, preferably 0.000005 to 0.0005%.
  • the steel of the present invention preferably further contains the following ingredients.
  • Cr has the effect of refining the pearlite and raising the strength of the steel.
  • the amount required for obtaining this effect is 0.05%. Addition of this or more is preferable. However, if adding over 1.0%, the ductility is impaired, so the upper limit is made 1.0%.
  • Ni strengthens the steel by effects similar to Cr. To obtain these effects, addition of 0.05% or more is preferable. If adding over 1.0%, the ductility falls, so the upper limit is made 1.0% or less.
  • Cu has the effect of improve the scale characteristics and corrosive fatigue characteristics of the wire. To obtain this effect, addition of 0.05% or more is preferable. If adding over 1.0%, the ductility falls, so the upper limit is made 1.0% or less.
  • Ti, Nb, and V have the effect of raising the strength of wire rod by precipitation strengthening. In each case, there is no effect if less than 0.001%, while if over 0.25%, precipitation embrittlement is caused. Accordingly, the content is made 0.001 to 0.25%. Further, these elements are effective if added to reduce the ⁇ grain size at the time of patenting.
  • Mo is an element which improves the hardenability of steel. In the case of the present invention, it is possible to raise the strength of the steel by adding this, but addition of an excessive amount causes the steel to excessively harden and makes working it difficult. Accordingly, the range of addition of Mo is made 0.05 to 1.0%.
  • Co by inclusion in 0.1 to 2%, has the effect of suppressing the formation of pro-eutectoid cementite of the hyper-eutectoid steel whereby the ductility is improved.
  • B improves the hardenability of steel and, when present in the austenite in the solid solution state, concentrates at the grain boundaries to suppress the formation of ferrite, degenerate pearlite, bainite, and other nonpearlite precipitates and thereby improve the drawability. If the amount of addition is too small, this effect cannot be obtained, so the lower limit is made 0.0005%. On the other hand, if adding too much, the precipitation of coarse Fe 3 (CB) 6 carbides in the austenite is promoted and the drawability is adversely influenced. Therefore, the upper limit is made 0.002%.
  • An REM is an element which influences the composition of inclusions of the present invention. If the REM is too great or too small, the predetermined composition of inclusions for improving the drawability cannot be obtained, so the content is made 0.000005 to 0.001%.
  • the steel of the present invention can be produced by tapping molten steel which has finished being refined in a converter or electric furnace into a ladle, then refining it by simplified ladle refining.
  • CAB capped argon bubbling
  • SAB shield argon bubbling
  • CAS adjusted of ingredients by SAB
  • the total oxygen amount in the steel 30 ppm or less it is effective to suppress as much as possible the contamination by converter slag which flows out from the converter to the ladle at the time of tapping and, further, to secure a sedation time of simplified ladle refining (time from end of ladle refining to start of continuous casting) of about 20 to 40 minutes, and to promote flotation and separation of oxides. Further, it is also effective to prevent oxidation by air of the molten steel between the ladle and the tundish and between the tundish and the continuous casting mold.
  • the melting of the synthetic slag and agitation of the molten steel, the secondary deoxidation and fine adjustment of ingredients and adjustment of molten steel temperature, and argon bubbling in the ladle are assumed to take 25 to 40 minutes. Further, argon bubbling in the ladle is used to uniformly mix the ingredients and cooling materials and promote the flotation and separation of inclusions.
  • usual Fe-Si contains about 1.5% of Al, but low Al-Fe-Si with an Al content of about 0.01 to 0.10% can be preferably used. Further, even if using refractories with a small alumina content as ladle refractories, it is effective to introduce inclusions with an (%Al 2 O 3 ) of 30% or less in a number ratio of 80% or more.
  • the (%CaO) and (%SiO 2 ) in the inclusions can be made ones in the ranges of the present invention by adjusting the contents of CaO and SiO 2 in the slag on the ladle in simplified ladle refining and by employing production conditions for making the total amount of oxygen in the above steel 30 ppm or less.
  • the ingredients and amounts of the SiO 2 -CaO-based synthetic slag which is added to the ladle so as to adjust the basicity of the ladle slag (CaO/SiO 2 mass ratio).
  • the basicity of the ladle slag is preferably 0.9 to 1.3. Further, by adopting production conditions giving a total oxygen amount in the steel of 30 ppm or less, it is possible to prevent an increase in the (%SiO 2 ) of inclusions due to oxidation of the Si ingredient in the steel.
  • the method of addition of Na and F may be to add them as an NaF compound or to add Na and F separately (for example, Na 2 CO 3 , CaF 2 , etc.) Note that, when adding F, if simultaneously adding it with metal Si, SiF 4 is formed and gasifies and the yield of F deteriorates, so this should be avoided.
  • the smelting of the present examples was performed by an LD converter.
  • a so-called “dart” type converter slag sealing tool is used to keep the outflow of LD slag at a small amount (50 mm thickness or less).
  • a carburization material for adjusting the ingredients of C, Si, and Mn and Fe-Si, Fe-Mn, Si-Mn, or other deoxidizing ferroalloy were added.
  • the deoxidizing ferroalloy one containing as little Al, Mg, or other powerful deoxidizing element as possible was used. Further, during the tapping or after the tapping, argon gas was blown in from the ladle bottom.
  • the molten steel in the ladle after receiving the steel was deoxidized by the Si, Mn, etc., that is, was so-called "killed steel".
  • This ladle was moved to the position for molten steel refining, then SiO 2 -CaO-based synthetic slag was added to the ladle, then argon was blown from the ladle bottom to agitate the molten steel in the ladle and perform CAB simplified ladle refining.
  • the secondary deoxidizing material was added to the molten steel as ferroalloy.
  • the secondary deoxidizing material included metal Ca, Al, Mg, Si, etc.
  • Na, F, and REM were added to the steel in the ladle.
  • NaF was added, when adding Na alone, Na 2 CO 3 was added, and when adding F alone, CaF 2 was added.
  • F it is added at a timing separate from the addition of the alloy containing Si or secondary deoxidizing material.
  • the ingredients were further finally adjusted and the refining of molten steel in the ladle was ended.
  • a suitable sedation time (20 to 40 minutes or so) so that the total oxygen amount in the steel becomes 16 to 30 ppm was secured, then continuous casting was performed.
  • the molten steel was continuously cast from the ladle through a tundish, but at that time, to suppress as much as possible the oxidation by air between the ladle and tundish and inside the tundish, inert gas was used to seal the system.
  • the obtained steel bloom was passed through a bloom heating furnace, then bloomed, the steel bloom was rolled to billet, and the steel billet was straightened, then it was passed through a heating furnace and rolled to produce 5.5 mm ⁇ wire rod.
  • the number and composition of nonmetallic inclusions were investigated by cutting out samples of 0.5 meter length from one coil of 5.5 mm ⁇ wire rod, cutting out small samples of 11 mm length from any 10 locations in the L direction (length direction), and investigating the entire surfaces at the longitudinal cross-sections passing through the center axes in the length direction.
  • the number and composition of nonmetallic inclusions were determined by obtaining oxide-based nonmetallic inclusions of a short axis of 0.5 ⁇ m or more, a long axis of 1.0 ⁇ m or more, and a circle equivalent diameter of 1 ⁇ m or more as "inclusions covered due to size" and analyzing the compositions of the individual inclusions by X-ray spectroscopy.
  • inclusions covered due to size the inclusions in the range of composition of the present invention are referred to as the "inclusions covered due to composition”. These were evaluated for the number ratio (number of inclusions covered due to composition/number of inclusions covered due to size ⁇ 100). Further, the average composition of all of the inclusions covered due to size was also calculated. However, for REM and S, the average composition of the inclusions covered due to composition was calculated.
  • wire breakage index The drawing characteristics were evaluated by the frequency of breakage for a certain amount of drawing as the "wire breakage index”. A wire breakage index of 5 or less was considered good.
  • the die life was evaluated indexed to the minimum lifetime allowable for materials in current processes as 100. The longer the lifetime, the greater the index. A die life index of 100 or more was good.
  • wires drawn to 0.175 mm ⁇ were subjected to rotating fatigue tests.
  • the stress was changed in various ways and the number of repetitions until breakage was investigated.
  • the stress at which wire breakage occurs with 100000 repetitions was corrected by the coefficient of tension of a mechanical test and evaluated as the stress index. A stress index of 15 or more was judged as good.
  • Tables 1 to 4 show the results of invention examples and comparative examples. Numerical values which are outside the ranges of the present invention are underlined. "Invention examples” 5 and 11 do not fall into the scope of the claimed high carbon steel wire rod of the present application.
  • Example Nos. 1 to 24 good results could be obtained in each case.
  • Nos. 8 to 18 are examples of addition of REMs in addition to Na and F. In this case, the die life and fatigue characteristics are improved.
  • Nos. 19 to 24 are examples of addition of B to the steel. A further improvement in the die life and fatigue characteristics was confirmed.
  • No. 25 is a case of no addition of Na and F
  • No. 26 is a case of addition of Na alone
  • No. 27 is a case of addition of F alone.
  • the number ratio of inclusions (number of inclusions covered due to composition/number of inclusions covered due to size ⁇ 100, below referred to as the "number ratio of inclusions") was zero.
  • the wire breakage index, die life, and fatigue characteristics all deteriorated compared with the invention examples.
  • No. 28 is the case where the seal in the tundish is insufficient, so the total oxygen amount becomes higher than the range of the present invention.
  • the number of inclusions was large and the die life and fatigue characteristics deteriorated.
  • Nos. 29 to 32 are examples where the number ratio of inclusions fell below 80%.
  • No. 29 is an example which uses refractories high in Al 2 O 3 and MgO content, so a large number of Al 2 O 3 -based and MgO-based inclusions believed to be due to the refractories are present in the inclusions. As a result, the number ratio of inclusions fell and the wire breakage index, die life, and fatigue characteristics all deteriorated.
  • No. 30 is an example where the change in composition of the SiO 2 -CaO-based synthetic slag caused the (%SiO 2 ) in the nonmetallic inclusions to drop, so the number ratio of inclusions fell, some hard inclusions appeared in the inclusions, and the wire breakage index, die life, and fatigue characteristics all deteriorated somewhat.
  • No. 31 is an example where the amount of outflow of LD slag was somewhat large, coarse inclusions of SiO 2 alone appeared in the deoxidizing process, and the (%SiO 2 ) in the nonmetallic inclusions increased. As a result, the number ratio of inclusions fell and the wire breakage index and fatigue characteristics deteriorated.
  • No. 32 is an example which used as a deoxidizing alloy not a low Al ferroalloy, but a high Al concentration usual ferroalloy.
  • the (%Al 2 O 3 ) in the nonmetallic inclusions increased.
  • the number ratio of inclusions fell, a large number of hard Al 2 O 3 -based inclusions were formed, and the wire breakage index, die life, and fatigue characteristics were all extremely poor.
  • No. 33 is an example where the concentration of S in the steel is high, the (%S) in the nonmetallic inclusions is a higher value than the range of the present invention, and the wire breakage index, die life, and fatigue characteristics deteriorate.
  • No. 34 is an example where has too much REM added, so the (%T.REM) in the nonmetallic inclusions becomes a value higher than the range of the present invention and the wire breakage index, die life, and fatigue characteristics deteriorate.

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EP12751796.9A 2011-03-01 2012-02-28 High-carbon steel wire rod excellent in drawability and fatigue characteristics after wire drawing Active EP2682489B1 (en)

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CN105438962B (zh) * 2015-12-31 2017-10-03 建峰索具有限公司 一种高强度钢丝绳浇铸索具
JP2017214652A (ja) * 2016-05-30 2017-12-07 株式会社フジクラ ガドリニウム線材、その製造方法、それを用いた金属被覆ガドリニウム線材、熱交換器及び磁気冷凍装置
BR112019017993A2 (pt) * 2017-03-24 2020-05-19 Nippon Steel Corp fio máquina e arame de aço plano
CN110760748B (zh) * 2018-07-27 2021-05-14 宝山钢铁股份有限公司 一种疲劳寿命优良的弹簧钢及其制造方法
CN109680121B (zh) * 2019-01-15 2020-10-23 北京科技大学 减少深拉拔切割钢丝中CaO-SiO2-Al2O3夹杂物的炼钢工艺
CN114075639A (zh) * 2020-08-20 2022-02-22 宝山钢铁股份有限公司 一种高强度高疲劳寿命缆索用钢、盘条及其制备方法
CN114657471B (zh) * 2022-03-27 2022-12-23 中天钢铁集团有限公司 一种低碳节能的≥2060MPa级桥梁缆索用盘条的生产方法

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EP2682489A1 (en) 2014-01-08
KR20130087618A (ko) 2013-08-06
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JP5310961B2 (ja) 2013-10-09
EP2682489A4 (en) 2014-08-20

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