WIRE ROD HAVING EXCELLENT DRAWABILITY, AND MANUFACTURING METHOD THEREFOR

Abstract

The present invention relates to a machine structure wire rod, which is applicable to vehicles, construction components and the like, and a manufacturing method therefor, and to a wire rod having excellent drawability, and a method for manufacturing same.

Description

TECHNICAL FIELD

The present invention relates to a mechanical structural wire rod, which is applicable to vehicles, construction components and the like, and a manufacturing method therefor, and to a wire rod having excellent drawability, and a method for manufacturing the same.

BACKGROUND ART

A mechanical structural steel material used in automobiles, construction parts, etc., such as bearings, is typically manufactured by drawing a rolled wire rod and cold working the rolled wire rod, into a complex shape.

However, since the steel material described above is a hypereutectoid steel, and is difficult to process, it is difficult to directly draw the rolled wire rod. For this purpose, a spheroidization softening heat treatment is performed, a material is sized through wire drawing, and then, an increase in strength due to wire drawing is corrected through an additional spheroidization softening heat treatment to prepare a soften material.

The spheroidization softening heat treatment described above is intended to improve cold workability, through such a spheroidization softening heat treatment, cementite in a microstructure is spheroidized, and distribution of homogeneous particles is induced. Thereby, it is possible to prevent disconnection during wire drawing, improve a lifespan of a processed dice, and reduce hardness of the material being processed.

However, when the above spheroidization softening heat treatment is performed, heat treatment costs may be high and an elongated production time may be required, which may cause an increase in manufacturing costs. In addition, it does not meet the recent demands of the times to minimize energy consumption for a reduction of carbon emissions. Therefore, in recent years, when providing a wire rod used in bearings, or the like, there is a demand for the development of wire rods that can secure excellent drawing characteristics while omitting or shortening the spheroidization softening heat treatment.

SUMMARY OF INVENTION

Technical Problem

An aspect of the present disclosure to provide a wire rod used in mechanical structural parts such as bearings, or the like, specifically, to a wire rod that can omit or shorten a spheroidization softening heat treatment, and secure drawing characteristics and strength, and a manufacturing method therefor.

The object of the present invention is not limited to the above. A person skilled in the art would have no difficulty in understanding the further subject matter of the present invention from the general content of this specification.

Solution to Problem

According to an aspect of the present disclosure, provided is a wire rod having excellent drawability, the wire rod including, by weight %: C: 0.8 to 1.2%, Si: 0.01 to 0.6%, Mn: 0.1 to 0.6%, Cr: 0.8 to 2.0%, Al: 0.01 to 0.06%, N: 0.02% or less (excluding 0), with a balance of Fe and inevitable impurities,

• • wherein a microstructure includes a pearlite main structure and proeutectoid cementite, and includes
  • at least 20 AlN particles with an average particle diameter of 30 nm or less per unit area (μm²) are included, and
  • the following Relational Expression 1 is satisfied.

(Average block grain size (μm))²/(Proeutectite cementite length (μm/1200 μm²))≤0.5  [Relational Expression 1]

According to another aspect of the present disclosure, provided is a method for manufacturing a wire rod having excellent drawability, the method including: heating a steel slab, including, by weight %: C: 0.8 to 1.2%, Si: 0.01 to 0.6%, Mn: 0.1 to 0.6%, Cr: 0.8 to 2.0%, Al: 0.01 to 0.06%, N: 0.02% or less (excluding 0), with a balance of Fe and inevitable impurities, and performing rolling on the steel slab to prepare a billet;

• • cooling the prepared billet;
  • heating the billet to a temperature of 950 to 1050° C.;
  • wire rolling the heated billet to a prepare a wire rod; and
  • winding the wire rod, cooling the wire rod at an average cooling rate of 3° C./sec or more to a temperature of 550 to 650° C., and cooling the same at an average cooling rate of 1° C./sec or less to a temperature of 550° C. to 650° C. or less,
  • wherein the wire rolling is performed so that an austenite grain size (AGS) is 5 to 20 μm before finish rolling, and the finish rolling is performed at a temperature range of 730° C. to Acm and a deformation amount of 0.3 or more.

Advantageous Effects of Invention

As set forth above, according to the present disclosure, a wire rod for mechanical structural parts such as bearings, or the like, having drawing characteristics and strength, even though a spheroidization softening heat treatment may be omitted or shortened, and a manufacturing method therefor may be provided. Thereby, cost reduction and carbon reduction effects in the manufacturing process may be achieved.

The various and beneficial advantages and effects of the present invention are not limited to the above-described content, and may be more easily understood through description of specific embodiments of the present disclosure.

BRIEF DESCRIPTION OF DRAWINGS

FIG. 1 is a photograph of the microstructure of Inventive Example 1 in an embodiment of the present disclosure observed with a scanning electron microscope (SEM).

FIG. 2 is a photograph of the microstructure of Comparative Example 5 in an embodiment of the present disclosure observed with a scanning electron microscope (SEM).

FIG. 3 is a photograph of the microstructure of Inventive Example 1 observed using Electron Backscatter Diffraction (EBSD) in an embodiment of the present disclosure.

FIG. 4 is a photograph of the microstructure of Comparative Example 5 observed using Electron Backscatter Diffraction (EBSD) in an embodiment of the present disclosure.

BEST MODE FOR INVENTION

Terms used in the present specification are for explaining specific exemplary embodiments rather than limiting the present disclosure. In addition, a singular form used in the present specification includes a plural form also, unless the relevant definition has a clearly opposite meaning thereto.

The meaning of “comprising” used in the specification is to embody the configuration and is not to exclude the presence or addition of other configurations.

Unless otherwise defined, all terms including technical terms and scientific terms used in the present specification have the same meaning as would be commonly understood by a person with ordinary skill in the art to which the present disclosure pertains. Pre-defined terms are interpreted as being consistent with the relevant technical literature and the disclosure herein.

Hereinafter, the present invention will be described in detail. The inventors of the present invention recognized that, in a wire rod used in mechanical structural parts such as bearings, or the like, when performing a spheroidization softening heat treatment, a lot of heat treatment costs and time are required, which acts as an environmental burden. Accordingly, even if the spheroidization softening heat treatment is shortened or omitted, the present inventors have conducted a method for securing excellent drawability for manufacturing parts in depth during wire drawing, thereby completing the present invention.

First, in an aspect of the present disclosure, a wire rod will be described in detail.

The wire rod of the present disclosure includes: by wt %, C: 0.8 to 1.2%, Si: 0.01 to 0.6%, Mn: 0.1 to 0.6%, Cr: 0.8 to 2.0%, Al: 0.01 to 0.06%, N: 0.02% or less (excluding 0), with a balance of Fe, and inevitable impurities. Hereinafter, a role and content of each component will be described. % for each component below refers to weight %.

Carbon (C): 0.8 to 1.2%

Carbon (C) is an element added to secure a certain level of strength. When a content of C is less than 0.8%, it may be difficult to secure sufficient strength even after quenching and tempering heat treatment after a spheroidization softening heat treatment and forging processing process due to a decrease in strength of a base material. When the content of C exceeds 1.2%, precipitates of a new phase such as (FeCr)₃C may cause a problem such as center segregation during solidification of a slab such as bloom, or the like. Therefore, the content of C is preferably 0.8 to 1.2%, and more preferably 0.9 to 1.1%.

Silicon (Si): 0.01 to 0.6%

Silicon (Si) is a representative substitutional element added to secure a certain level of strength. When a content of Si is less than 0.01%, it may be difficult to secure strength of steel and sufficient hardenability. When the content of Si exceeds 0.6%, there is a disadvantage in that cold forgeability deteriorates during forging after the spheroidization softening heat treatment. Therefore, the content of Si is preferably 0.01 to 0.6%.

Manganese (Mn): 0.1 to 0.6%

Manganese (Mn), as an element that enhances solid solution strengthening by forming a substitutional solid solution in a matrix structure, is an element that can secure a desired degree of strength without deteriorating ductility, and is a representative austenite former. When a content of Mn is less than 0.1%, strength through solid solution strengthening is not guaranteed, and it is difficult to expect an improvement in toughness. In addition, when the content of Mn exceeds 0.6%, defects such as chevron cracks may occur due to MnS during forging after the spheroidization softening heat treatment. Therefore, the content of Mn is preferably 0.1 to 0.6%.

Chromium (Cr): 0.8 to 2.0%

Chromium (Cr), like Mn, is an element improving hardenability of steel. When a content of Cr is less than 0.8%, it may be difficult to secure sufficient hardenability to obtain martensite during hardening and tempering heat treatment after a forging process. When the content of Cr exceeds 2.0%, there may be a high possibility of a large amount of low-temperature structures occurring in a wire rod increases due to central segregation. Accordingly, the content of Cr is preferably 0.8 to 2.0%, and more preferably 1.0 to 2.0%.

Aluminum (Al): 0.01 to 0.06%

Aluminum (Al) is an element that not only has a deoxidizing effect, but also helps in inhibiting austenite grain growth and ensuring a fraction of proeutectoid ferrite to be close to an equilibrium phase by precipitating Al-based carbonitrides. When a content of Al is less than 0.01%, dissolved aluminum is not sufficient, so most of the Al is dissolved, and aluminum nitride (AlN), which inhibits austenite grain growth during heat treatment, is not sufficiently generated, so the content of Al is preferably 0.01% or more. Meanwhile, when the content of Al exceeds 0.06%, hard inclusions such as Al₂O₃, or the like, may increase, and in particular, nozzle clogging due to inclusions may occur during continuous casting. Therefore, the content of Al is preferably 0.01 to 0.06%.

Nitrogen (N): 0.02% or less (excluding 0%)

Nitrogen (N) is an element having a solid solution strengthening effect, but when a content of N exceeds 0.02%, toughness and ductility of a material may decrease due to dissolved nitrogen, which is not combined with nitride, so the content of N is preferably 0.02% or less.

The wire rod according to an aspect of the present disclosure may include a balance of Fe and other inevitable impurities in addition to the components described above. However, in a general manufacturing process, unintended impurities may inevitably be mixed from a raw material or the surrounding environment, and thus, these impurities may not be completely excluded. Since these impurities are known to those skilled in the art, all the contents are not specifically mentioned in the present specification. In addition, additional addition of effective components other than the above-described components is not entirely excluded.

Meanwhile, the microstructure of the wire rod according to an aspect of the present disclosure, includes a pearlite main structure and proeutectoid cementite. Specifically, the proeutectoid cementite is formed in a network shape at grain boundaries along prior austenite grains, and generated pearlite is formed within the grain boundaries. During cooling, supersaturated carbon in austenite is precipitated as Fe₃C, and proeutectoid cementite is formed at the grain boundaries of prior austenite. Due to refinement of grains, which is a diffusion path of elements, proeutectoid cementite has a network shape.

AlN is precipitated within the microstructure, and it is preferable that 20 or more AlN particles with an average particle diameter of 30 nm or less are distributed per unit area (μm²). If the average particle diameter of AlN exceeds 30 nm, an effect of inhibiting grain growth due to pinning is significantly reduced, so it is preferable to have a size of 30 nm or less. If AlN particles are present in an amount of less than 20 per unit area (μm²), even though AlN particles is generated, the number of AlN particles is not sufficient to suppress grain growth, so grain coarsening may occur. It is more preferable that the number of AlN particles having a size of 30 nm or less per unit area (μm²) is 50 or more,

Meanwhile, the pearlite and proeutectoid cementite preferably includes, by area fraction: 10% or less of proeutectoid cementite, with a remainder of pearlite, and may further include one or more of 5% or less of one or more of proeutectoid ferrite, bainite, and martensite. When a fraction of proeutectoid cementite exceeds 10%, toughness may rapidly decrease, so the fraction thereof is preferable not to exceed 10%. Meanwhile, during a process of manufacturing a wire rod, one or more of proeutectoid ferrite, bainite, and martensite may be generated to some extent, but when the fraction exceeds 5%, breakage may easily occur during drawing, so the fraction is preferable not to exceed 5%.

During a spheroidization softening heat treatment, the characteristics of grain boundaries are a major factor in determining a diffusion rate and serve to determine a total heat treatment time. During the softening heat treatment, cementite in a pearlite structure changes a shape thereof from plate-like to spherical, and strength of a material decreases depending on a degree of spheroidization.

During the softening heat treatment, metal atoms move through various diffusion paths through defect spaces in a material, and diffuse through a vacancy, which is an atomic defect, and dislocations or pipes, which are a type of line defect, grain boundaries, and the like. Compared to atomic defects, dislocations and grain boundaries have a relatively large space, which is advantageous for rapid diffusion.

In order to omit the softening heat treatment or shorten the time, it is preferable to increase an area of relative grain boundaries through grain refinement, but adverse effects such as reduced equipment life, productivity, and the like, due to an increase in rolling load may occur. Accordingly, the wire rod of the present disclosure has a microstructure satisfying the following Relational Expression 1, so that a wire rod with excellent drawability may be obtained even if the spheroidization softening heat treatment is omitted or shortened.

$\left[\mathrm{Relational}\mathrm{Expression}1\right]$ ${\left(\mathrm{Average}\mathrm{block}\mathrm{grain}\mathrm{size}\left(\mu m\right)\right)}^2\text{⁠}/\mathrm{Proeutectite}\mathrm{cementite}\mathrm{length}\left(\mu m/1200\mu m^2\right))\le 0.5$

The block grains refer to a group of grains with the same orientation of ferrite among cementite and ferrite constituting pearlite, and an average size thereof refers to an average particle diameter of the grains.

A length of the proeutectoid cementite refers to a total length of the proeutectoid cementite measured in a unit area (1200 μm²). As described above, since the proeutectoid cementite is formed along prior austenite grain boundaries, a length of the proeutectoid cementite preferably refers to a length measured along the grain boundaries.

The wire rod of the present disclosure may be drawn by at least 15% without a spheroidization softening heat treatment before a drawing process, wherein the wire rod has a tensile strength (TS) of 1200 MPa or more, and a reduction rate of cross-sectional area of 20% or more. The wire rod of the present disclosure may be drawn even if the spheroidization softening heat treatment is omitted. Due to a coarse grain size of commonly used materials, defects such as chevron cracks may occur even with a drawing amount of around 10%. However, the wire rod of the present disclosure does not have defects such as cracks thereinside, even with a drawing amount of exceeding 15%, or approximately 30%. This is because it is easy to rotate a colony when applying wire drawing, thereby relieving external stress and preventing defects such as cracks from occurring with a small amount of wire drawing. In addition, as the amount of wire drawing increases, vacancies such as dislocations and vacancies are created, further promoting spheroidization behavior during the spheroidization softening heat treatment after wire drawing.

In order to manufacture mechanical parts such as bearing steel with a complex shape, or the like, wire rods are manufactured into steel wires, which usually apply two spheroidization softening heat treatments and a drawing process for sizing the material. A typical spheroidization softening heat treatment is performed at a temperature of Ae1 to Ae1+100° C., and is a heat treatment method in which carbides with an average aspect ratio of cementite of 3 or less are generated in an entire region from a surface to a center portion after the heat treatment. However, the wire rod of the present disclosure may provide a greater amount of wire drawing than conventional materials through improved drawability through manufacturing a fine-grained wire rod, and promotes generation of spheroidized cementite during spheroidization heat treatment, so cementite having an average aspect ratio of less than 3 and a low tensile strength of less than 740 MPa is obtained with just one spheroidization heat treatment after drawing. Thus, cold forging or cold forging processing for manufacturing a final product may be facilitated.

Next, a method for manufacturing a wire rod, according to another aspect of the present disclosure will be described in detail. As a preferred example of manufacturing the wire rod of the present disclosure, a steel slab having the above-described alloy composition, for example, a bloom, may be heated and the steel slab may be rolled to manufacture a billet, and the billet may be heated, wire rolled, and cooled to manufacture the wire rod of the present disclosure. Hereinafter, each step is described in detail.

First, a steel slab having the above-described alloy composition, for example, a bloom is prepared, and heated to a temperature of 1100 to 1300° C. When a heating temperature of the steel slab is lower than 1100° C., the temperature is low and is not sufficient to diffuse elements in the steel slab, making it difficult to eliminate a concentrated segregation layer created during continuous casting. Meanwhile, when the temperature exceeds 1300° C., scales may be formed on a surface of the steel slab at a rapid rate, so that surface flaws may occur during rolling, or productivity may decrease due to material loss. Meanwhile, the heating time of the steel slab is preferably 2 to 10 hours, and if the heating time of the steel slab is less than 2 hours, it is difficult to reach a target temperature even inside the steel slab, and if the heating time exceeds 10 hours, a depth of a surface decarburization layer increases and the decarburization layer may remain even after finishing rolling, so it is preferable that the heating time does not exceed 10 hours.

A billet is manufactured by rolling the heated steel slab. The billet manufactured after rolling the steel slab is generally cooled to room temperature through air cooling, but in the present disclosure, a billet having a temperature of 500° C. or more is cooled at a cooling rate of 5° C./s or more. For this purpose, water cooling is preferably performed, and as a specific example, it is preferably charged into a water cooling chamber to prevent precipitation and coarsening of AlN as much as possible. When a billet having a temperature of 500° C. or less, AlN precipitates and coarsens, making it difficult to secure AlN of 30 nm or less because AlN is not sufficiently dissolved during heating a billet for manufacturing a wire rod, which is the next process.

The prepared billet is heated to a temperature within a range of 950 to 1050° C. When the billet heating temperature is less than 950° C., rolling properties may deteriorate, and when the billet heating temperature exceeds 1050° C., rapid cooling is required for rolling, so that not only is cooling control difficult, but it can also be difficult to ensure good product quality, due to occurrence of cracks, or the like. The heating time is preferably 80 to 120 minutes. If the heating time is less than 80 minutes, it is difficult to reach a target temperature even inside the material, and an atmosphere in which reverse transformation is not completed may partially occur. If it exceeds 120 minutes, a depth of a surface decarburization layer increases and the decarburization layer may remain after finishing rolling, which is not preferable.

The heated billet is wire-rolled to obtain a wire rod. It is preferable that wire rod rolling is groove rolling causing the billet to have a form of a wire rod. In the present disclosure, it is preferable that an austenite grain size (AGS) before finish rolling is 5 to 20 μm. Thereafter, finish rolling is preferably performed at a temperature within a range of 730° C. to Acm with a deformation amount of 0.3 or more. It is more preferable that the deformation amount is 0.5 or more. Here, Acm refers to a temperature at which cementite dissolves during heating or precipitates during cooling in hypereutectoid steel.

If the AGS before the finish rolling is less than 5 μm, there may be a problem that roll load increases, so that a lifespan of equipment is shortened because it is implemented through rough rolling at a low temperature. If the AGS before the finish rolling exceeds 20 μm, it may be difficult to manufacture a wire rod with fine grains because an increase in critical deformation is required during finish rolling. In addition, when the finish rolling temperature is lower than 730° C., rolling roll load may increase, so that the equipment life is shortened, and when the finish rolling temperature is higher than Acm, phase transformation does not occur, making it difficult to manufacture fine-grained wire rods.

Meanwhile, when rolling the wire rod, it is preferable to satisfy the conditions of the following Relational Expression (2).

$\left[\mathrm{Relational}\mathrm{Expression}2\right]$ $2500*{\left(\left[C\right]-1\right)}^2+100000*{\left(\left[A1\right]-0.035\right)}^2+{\left(\mathrm{AGS}-12.5\right)}^4/130+{\left(\mathrm{Finish}\mathrm{rolling}\mathrm{temperature}-760\right)}^2/65\le 80$

In the above Relational Expression (2), [C] and [Al] refer to an alloy composition C and Al content (% by weight), a unit of AGS is μm, and a unit of finish rolling temperature is ° C.

A content of carbon affects formation of cementite (Fe₃C) in a prepared wire rod and spheroidized heat-treated material, which affects mechanical properties such as tensile strength, or the like, so it is required to contain an appropriate amount of carbon. As an amount of Al decreases, an amount of AlN precipitated decreases and grain growth cannot be suppressed, so an optimal amount thereof is required. In addition, the larger the AGS before finish rolling, the lower a rolling amount and finish rolling temperature should be to reduce the grain size, so it is preferable to manage an appropriate AGS and finish rolling temperature from a perspective of process costs. Relational Expression 2 reflects this technical viewpoint, and when a value thereof in Relational Expression 2 exceeds 80, it is difficult to expect appropriate cementite formation and grain refinement effects.

After the wire rod rolling, the wire rod is wound and cooled. The cooling is preferably performed at an average cooling rate of 3° C./sec or more until a temperature range of 550 to 650° C., and then after the temperature of 550 to 650° C., cooling is preferably performed at an average cooling rate of 1° C./sec or less. When the average cooling rate until the temperature range of 550 to 650° C. is less than 3° C./sec, it is difficult to maintain fine grains secured during rolling below a transformation point. Meanwhile, after reaching the temperature of 550 to 650° C., a cooling rate therebelow is preferably 1° C./sec or less in terms of suppressing low-temperature structures such as bainite and martensite.

In the present disclosure, after drawing the wire rod prepared as above, the wire rod may be heated to Ae1 to Ae1+100° C. and maintained for 5 to 15 hours, and then subjected to a spheroidization heat treatment by being cooled to 660° C. at 20° C./hr or less to prepare a spheroidized material. When the heating temperature is less than Ae1, there may be a disadvantage in that a spheroidization heat treatment time becomes longer, and when the heating temperature exceeds Ae1+100° C., an effect of the spheroidization heat treatment may not be sufficient because spheroidization carbide seeds are reduced. Here, Ae1 refers to a temperature at which austenite is generated during heating, or at which austenite disappears during cooling. When the holding time is less than 5 hours, there may be a disadvantage in that an aspect ratio of cementite increases because the spheroidization heat treatment does not proceed sufficiently, and when the holding time exceeds 15 hours, there may be a disadvantage in that costs increase. When the heating temperature exceeds 20° C./hr, there may be a disadvantage in that pearlite is reformed due to a rapid cooling rate. After the spheroidization heat treatment, a wire rod has a low tensile strength of 740 MPa or less and an average cementite aspect ratio of 3 or less, which can facilitate cold forging or cold forging processing to manufacture a final product.

MODE FOR INVENTION

Hereinafter, the present disclosure will be specifically described through the following Examples. However, it should be noted that the following examples are only for describing the present disclosure by illustration, and not intended to limit the right scope of the present disclosure. The reason is that the right scope of the present disclosure is determined by the matters described in the claims and reasonably inferred therefrom.

EXAMPLE

A steel slab (bloom) having alloy compositions (% by weight, a balance of Fe and inevitable impurities) shown in Table 1 below was prepared, and then was subjected to steel slab rolling to manufacture a billet. After continuous casting, the steel slab was subjected to homogenization heat treatment at 1200° C. for 4 hours and then rolled at 1000° C. In the case of water cooling according to the cooling method disclosed in Table 2 after the steel slab rolling, the steel slab was air cooled to a temperature of 500° C. and then charged into a water cooling chamber and cooled at a cooling rate of 5° C./s or more. Thereafter, the manufactured billet was manufactured into a wire rod having a diameter of 9 mm under the wire rod manufacturing conditions disclosed in Table 2 below. The microstructure and mechanical properties of the thus prepared wire rod was measured, and the results were shown in Table 3. Meanwhile, after drawing the prepared wire rod, an average aspect ratio and tensile strength of cementite were measured by one soft spheroidization heat treatment (maintained at 780° C. for 8 hours and then cooled to 640° C. at a cooling rate of 15° C./hr), and the results were shown in Table 4.

Meanwhile, in Table 2, an austenite grain size (AGS) before finish rolling was collected by cutting a material through a cutting crop performed before finish hot rolling, and immediately quenching the same in water, and AGS was measured using an ASTM E112 method. For the collected specimens, five arbitrary ¼ points from the diameter were measured and then expressed as an average value.

An average block grain size was measured using EBSD and ASTM E112 methods. A block is a region where a crystal orientation of ferrite within pearlite is the same, and a size having a crystal orientation difference of at least 15 degrees was defined as a block size. Among the following examples, Inventive Example 1 and Comparative Example 5 were observed and shown in FIGS. 3 and 4, respectively. The size of the block was quantified using the ASTM E112 method. For a specimen collected after removing an unwater-cooling portion after rolling a wire rod, the measured material was measured at five arbitrary ¼ points from the diameter, and then expressed as an average value. In addition, for a specimen collected after removing an unwater-cooling portion after rolling a wire rod, a length of proeutectoid cementite was photographed at five arbitrary ¼ points from the diameter at ×3000 using an SEM, and a total length of proeutectoid cementite was analyzed using measured using Leica's Clemex vision software, and an average of the 5 points was obtained.

Drawability was evaluated by drawing the prepared wire rod having a diameter of 9 mm at a cross-sectional reduction rate of 5 to 50%, and a center portion of a L cross-section of the drawn material was photographed at 5,000× magnification to check whether defects such as chevron cracks occurred at a pearlite interface or proeutectoid cementite interface, and whether cracks occurred or did not occur was indicated as O/X.

Meanwhile, the average aspect ratio of cementite after the one-time spheroidization heat treatment was measured by photographing ¼ to ½ points in a diameter direction of the wire rod at 3,000× magnification using a SEM in 3 fields of view, automatically measuring a long axis/short axis of cementite within the field of view using an image measurement program, and then performing statistical processing.

TABLE 1
Steel type	C	Si	Mn	Cr	Al	N
Steel	1.05	0.29	0.30	1.69	0.023	0.006
type 1
Steel	1.01	0.28	0.35	1.33	0.024	0.005
type 2
Steel	0.96	0.25	0.35	1.36	0.023	0.004
type 3
Steel	1.00	0.25	0.33	1.36	0.027	0.006
type 4
Steel	0.95	0.24	0.33	1.39	0.029	0.005
type 5
Steel	1.00	0.30	0.27	1.51	0.025	0.003
type 6
Steel	0.97	0.23	0.33	1.41	0.003	0.006
type 7
Steel	0.50	0.20	0.27	1.48	0.023	0.006
type 8
Steel	0.97	0.20	0.32	1.34	0.030	0.003
type 9
Steel	1.04	0.22	0.27	1.57	0.030	0.003
type 10
Steel	0.98	0.23	0.27	1.65	0.026	0.003
type 11
Steel	0.98	0.28	0.30	1.50	0.024	0.007
type 12
Steel	1.03	0.25	0.27	1.60	0.021	0.007
type 13

TABLE 2
		Cooling							Cooling
		method			Before				speed	Cooling
		after	Billet	Billet	finish	Finish	Finish		to a	speed
		rolling	heating	heating	rolling	rolling	rolling		temperature	after
Steel		steel	temperature	time	AGS	temperature	deformation	Relational	of 600° C.	600° C.
type	Division	slab	(° C.)	(min.)	(μm)	(° C.)	rate	Expression 2	(° C./sec)	(° C./sec)
Steel	Inventive	Water	960	83	10	779	0.6	28	3.2	0.6
type 1	example 1	cooling
Steel	Inventive	Water	1030	92	12	769	1	14	4.7	1
type 2	example 2	cooling
Steel	Inventive	Water	1050	105	8	761	0.5	22	4.9	1
type 3	example 3	cooling
Steel	Inventive	Water	1003	110	7	773	1	16	3.6	0.8
type 4	example 4	cooling
Steel	Inventive	Water	955	97	10	754	0.5	11	4.4	0.7
type 5	example 5	cooling
Steel	Comparative	Air	959	99	12	769	1	11	3.5	0.6
type 6	Example 1	cooling
Steel	Comparative	Water	1049	83	8	746	0.8	111	4.3	0.8
type 7	Example 2	cooling
Steel	Comparative	Water	1014	105	7	739	0.6	654	3.8	0.9
type 8	Example 3	cooling
Steel	Comparative	Water	1237	85	24	747	0.9	142	3.5	0.7
type 9	Example 4	cooling
Steel	Comparative	Water	1050	99	12	876	0.5	214	4.9	1
type 10	Example 5	cooling
Steel	Comparative	Water	982	88	11	758	0.2	10	3	0.6
type 11	Example 6	cooling
Steel	Comparative	Water	977	94	12	760	0.5	13	1.2	0.5
type 12	Example 7	cooling
Steel	Comparative	Water	968	105	10	761	1	22	3.7	5
type 13	Example 8	cooling

In Table 2, Relational Expression 2 is calculated by 2500*([C]−1)²+100000*([Al]−0.035)²+(AGS−12.5)⁴/130+(finish rolling temperature−760)²/65, where [C] and [Al] are contents of C and Al (& by weight) in an alloy composition, AGS is an average austenite grain size, a unit is μm, and a unit of the finish rolling temperature is ° C.

TABLE 3
		The number	Block				Cross-
		of AlN,	grain	Length of			sectional
		less than	average	proeutectoid		Tensile	reduction
		30 nm, per	size	(μm/1200	Relational	strength	rate
Division	Microstructure	μm2	(μm)	μm2)	Expression 1	(MPa)	(%)
Inventive	Proeutectoid	67	4.7	212	0.10	1270	28
example 1	C + P
Inventive	Proeutectoid	90	3.2	206	0.05	1251	35
example 2	C + P
Inventive	Proeutectoid	68	6.4	225	0.18	1239	26
example 3	C + P
Inventive	Proeutectoid	69	3	241	0.04	1262	37
example 4	C + P
Inventive	Proeutectoid	71	7.2	156	0.33	1292	31
example 5	C + P
Comparative	Proeutectoid	13	10.2	63	1.65	1178	17
Example 1	C + P
Comparative	Proeutectoid	16	9.7	67	1.40	1182	19
Example 2	C + P
Comparative	Proeutectoid	76	4.3	230	0.08	850	31
Example 3	C + P
Comparative	Proeutectoid	60	12.4	70	2.20	1157	17
Example 4	C + P
Comparative	Proeutectoid	86	11.6	62	2.17	1162	19
Example 5	C + P
Comparative	Proeutectoid	79	12.1	57	2.57	1171	16
Example 6	C + P
Comparative	Proeutectoid	69	9	112	0.72	1192	19
Example 7	C + P
Comparative	Proeutectoid	48	Cannot be	192	Cannot be	1491	12
Example 8	C + P +		measured		measured
	B + M

In Table 3, proeutectoid C refers to proeutectoid cementite, P refers to pearlite, B refers to bainite, and M refers to martensite. In addition, Relational Expression 1 refers to an average block grain size (μm))²/(proeutectoid cementite length (μm/1200 μm²)).

	TABLE 4
	Microstructure and
	mechanical
	properties after a
	drawing amount of
	applied thereto and
	spheroidization heat
	treatment
	Amount	Average
	of wire	aspect	Tensile
	rod	ratio of	strength
	before	cementite	after
	Whether cracks occur inside a	spheroidization	after	spheroidization
	material depending on a	heat	spheroidization	heat
Division	drawing amount (%)	treatment	heat	treatment
	5	10	15	20	30	40	50	(%)	treatment	(MPa)
Inventive	◯	◯	◯	◯	◯	◯	X	30	1.7	716
example 1
Inventive	◯	◯	◯	◯	◯	◯	◯	20	2.3	724
example 2
Inventive	◯	◯	◯	◯	◯	◯	◯	40	2.5	721
example 3
Inventive	◯	◯	◯	◯	◯	X	X	30	2.5	730
example 4
Inventive	◯	◯	◯	◯	◯	◯	X	40	1.6	726
example 5
Comparative	◯	X	X	X	X	X	X	5	5.7	811
Example 1
Comparative	◯	◯	X	X	X	X	X	10	6.1	807
Example 2
Comparative	◯	◯	◯	◯	◯	◯	X	40	2.3	607
Example 3
Comparative	◯	X	X	X	X	X	X	5	7.3	813
Example 4
Comparative	◯	X	X	X	X	X	X	5	6.2	827
Example 5
Comparative	◯	X	X	X	X	X	X	5	6.9	832
Example 6
Comparative	◯	◯	X	X	X	X	X	10	5.8	789
Example 7
Comparative	X	X	X	X	X	X	X	0	7.6	812
Example 8

As can be seen from Tables 1 to 4 above, the wire rods of Inventive examples 1 to 5 satisfying the conditions proposed by the present disclosure may secure excellent drawability with a cross-sectional reduction rate of 20% or more even without spherical softening heat treatment, and at the same time, may secure high strength of 1200 MPa or more. In addition, a wire rod having an average cementite aspect ratio of 3 or less may be provided with just one spheroidization heat treatment after drawing processing. In particular, FIG. 1 is a photograph of a microstructure of the wire rod of Inventive Example 1 observed using a scanning electron microscope (SEM). Referring to FIG. 1, in Inventive Example 1, the microstructure of the wire rod is composed of proeutectoid cementite and generated pearlite, and in FIG. 1, an arrow indicates proeutectoid cementite. As shown in FIG. 1, it can be confirmed that proeutectoid cementite is formed along prior austenite grain boundaries. FIG. 3 is an EBSD photograph of Inventive Example 1, and it can be confirmed that a grain orientation difference is at least 2 degrees, and an average block grain size of Inventive Example 1 is about 4.7 μm, which is very small compared to normal manufacturing conditions.

Meanwhile, in Comparative Example 1, air cooling was performed after rolling a steel slab, so AlN in a steel material became coarse, and in Comparative Example 2, an AlN content in the steel composition was low, so AlN was hardly produced. As a result, in the wire rods of Comparative Examples 1 and 2, the number of AlN with a size of 30 nm or less per μm² was 20 or less, and grain growth was not suppressed during cooling the wire rod, so that the size of block grains was not controlled. In Comparative Example 3, it has a low carbon content, and proeutectoid ferrite remains in a wire rod, so drawing characteristics were superior to those of other Comparative Example, but the strength was low due to the low carbon content, which makes it difficult to use for the intended purpose due to the low strength of the material even after spheroidization heat treatment.

In Comparative Example 4, a size of AGS before finish rolling is larger than that of the Inventive examples due to a high billet heating temperature. Since coarse AGS can be grain refined through a high critical deformation rate, insufficient finish rolling deformation rate, eventually causes coarse grains to appear in the wire rod, resulting in poor drawability. In Comparative Example 5, fine grains were not obtained due to a high finish rolling temperature, and, like Comparative Example 4, the drawing characteristics were not excellent due to the coarse grains. FIG. 2 is a photograph of a microstructure of the wire rod of Comparative Example 5 observed with an SEM, and it can be confirmed that crystal grains are larger in size and a length of proeutectoid cementite produced along prior austenite grain boundaries is shorter compared to FIG. 1. FIG. 4 is an EBSD photograph of Comparative Example 5, in which a grain orientation difference was distinguished as in FIG. 3. Compared with FIG. 3, it can be seen that in Comparative Example 5 of FIG. 4, a block grain size was coarse.

In Comparative Example 6, fine grains were not obtained due to a small amount of finish rolling, and coarse grains appeared in the wire rod, resulting in poor drawing characteristics. In the wire rod of Comparative Example 7, the fine grains produced by rolling were coarsened due to a low initial cooling rate, so fine wire rod grains were not obtained, resulting in poor drawing characteristics. In the case of Comparative Example 8, martensite and bainite appeared due to a fast cooling rate, so that it could be confirmed that internal cracks occurred with only 5% drawing.

While example embodiments have been illustrated and described above, it will be apparent to those skilled in the art that modifications and variations could be made without departing from the scope of the present disclosure as defined by the appended claims.

Claims

1. A wire rod having excellent drawability including by weight %: [ Relational ⁢ Expression ⁢ 1 ] ( Average ⁢ block ⁢ grain ⁢ size ⁢ ( μ ⁢ m ) ) 2 ⁠ / Proeutectite ⁢ cementite ⁢ length ⁢ ( μ ⁢ m / 1200 ⁢ μ ⁢ m 2 ) ) ≤ 0.5

C: 0.8 to 1.2%, Si: 0.01 to 0.6%, Mn: 0.1 to 0.6%, Cr: 0.8 to 2.0%, Al: 0.01 to 0.06%, N: 0.02% or less (excluding 0), with a balance of Fe and inevitable impurities,

wherein a microstructure includes a pearlite main structure and proeutectoid cementite, and includes at least 20 AlN particles with an average particle diameter of 30 nm or less per unit area (μm2), and

the following Relational Expression 1 is satisfied,

2. The wire rod having excellent drawability of claim 1, wherein the proeutectoid cementite is formed at grain boundaries along prior austenite grains, and is formed in a network shape.

3. The wire rod having excellent drawability of claim 1, wherein the microstructure comprises, by area fraction: 10% or less of proeutectoid cementite and a balance of pearlite.

4. The wire rod having excellent drawability of claim 1, wherein the wire rod has a tensile strength of 1200 MPa or more and a cross-sectional reduction rate of 20% or more.

5. The wire rod having excellent drawability of claim 1 wherein the wire rod is not subjected to a spheroidization softening heat treatment before a drawing process, and is drawn by at least 15% during wire drawing.

6. The wire rod having excellent drawability of claim 1, wherein the wire rod has an average aspect ratio of cementite of 3 or less after the wire drawing and spheroidization heat treatment.

7. A method for manufacturing a wire rod having excellent drawability, comprising:

heating a steel slab, including by weight:

C: 0.8 to 1.2%, Si: 0.01 to 0.6%, Mn: 0.1 to 0.6%, Cr: 0.8 to 2.0%, Al: 0.01 to 0.06%, N: 0.02% or less (excluding 0), with a balance of Fe and other inevitable impurities, and performing rolling on the steel slab to prepare a billet;

cooling the prepared billet;

heating the billet to a temperature of 950 to 1050° C.;

wire rolling the heated billet to a prepare a wire rod; and

winding the wire rod, cooling the wire rod at an average cooling rate of 3° C./sec or more to 550 to 650° C., and cooling the same at an average cooling rate of 1° C./sec or less to a temperature of 550° C. to 650° C. or less,

wherein the wire rolling is performed so that an austenite grain size (AGS) is 5 to 20 μm before finish rolling, and the finish rolling is performed at a temperature range of 730° C. to Acm and a deformation amount of 0.3 or more.

8. The method for manufacturing a wire rod having excellent drawability of claim 7, wherein the hot rolling is performed to satisfy the condition of Relational Expression (2) below, [ Relational ⁢ Expression ⁢ 2 ] 2500 * ( [ C ] - 1 ) 2 + 100000 * ( [ A ⁢ 1 ] - 0.035 ) 2 + ( AGS - 12.5 ) 4 / 130 + ( Finish ⁢ rolling ⁢ temperature - 760 ) 2 / 65 ≤ 80 in the above Relational Expression (2), [C] and [Al] refer to an alloy composition C and Al content (% by weight), a unit of AGS is μm, and a unit of finish rolling temperature is ° C.

9. The method for manufacturing a wire rod having excellent drawability of claim 7, wherein the billet is heated to a temperature within a range of 1100 to 1300° C. for 2 to 10 hours, and the billet having a temperature of 500° C. or more at a cooling rate of 5° C./s or more after the billet is rolled.

10. The method for manufacturing a wire rod having excellent drawability of claim 7, wherein the billet heating time is 80 to 120 minutes.