HIGH-STRENGTH WIRE ROD FOR COLD HEADING WITH SUPERIOR HEAT TREATMENT CHARACTERISTICS AND RESISTANCE OF HYDROGEN-DELAYED FRACTURE CHARACTERISTICS, HEAT-TREATED COMPONENT, AND METHOD FOR MANUFACTURING SAME

- POSCO CO., LTD

Disclosed in the present specification are: a high-strength wire rod for cold heading, having superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics, the rod being applicable to a bolt, etc.; a heat-treated component; and a method for manufacturing the same. According to an exemplary embodiment, the high-strength wire rod for cold heading with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics comprises, by wt %, 0.3-0.6% of C, 0.05-0.3% of Si, 0.2-1.0% of Mn, 0.5-2.0% of Cr, 0.5-2.0% of Mo, 0.02-0.05% of Al, 0.01-0.03% of N, and Fe and other impurities as the balance, and has a microstructure comprising, by area fraction, 80% or more of bainite, 1-15% of pearlite and 0.1-2% of martensite, and comprises 2×1019/m3 or more of aluminum nitride having a diameter of 5-50 nm.

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Description
TECHNICAL FIELD

The present disclosure relates to a high-strength wire rod for cold heading with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics, a heat-treated component, and a method for manufacturing the same. More particularly, it relates to a high-strength wire rod for cold heading with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics, which is applicable to a high-strength bolt, etc., a heat-treated component, and a method for manufacturing the same.

BACKGROUND ART

In general, wire rods for cold heading are classified into process-eliminated wire rods for cold heading with heat treatment and machining processes eliminated and high-strength wire rods for cold heading that allow weight reduction of components.

The high-strength wire rod for cold heading is manufactured by cold-heating a wire rod after spheroidization heat treatment, and then it is prepared into a heat-treated component such as a mechanical structure, an automobile part, etc. through quenching and tempering.

However, the metal structure of a general wire rod is mainly composed of pearlite, and there is an inconvenience in that heat treatment for a long time is required to dissolve cementite during austenitization heat treatment.

In addition, a tempered martensite microstructure is formed when austenitization heat treatment is performed. It is difficult to use the tempered martensite microstructure because it is very sensitive to resistance of hydrogen-delayed fracture at 1300 MPa or higher.

Accordingly, it is necessary to develop a high-strength wire rod for cold heading with superior resistance of hydrogen-delayed fracture characteristics at 1300 MPa or higher.

DISCLOSURE Technical Problem

The present disclosure is directed to providing a high-strength wire rod for cold heading with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics, a heat-treated component, and a method for manufacturing the same.

Technical Solution

The present disclosure provides a high-strength wire rod for cold heading with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics, which comprises, by wt %, 0.3-0.6% of C, 0.05-0.3% of Si, 0.2-1.0% of Mn, 0.5-2.0% of Cr, 0.5-2.0% of Mo, 0.02-0.05% of Al, 0.01-0.03% of N, and Fe and other impurities as the balance, and has a microstructure comprising, by area fraction, 80% or more of bainite, 1-15% of pearlite and 0.1-2% of martensite, and comprises 2×1019/m3 or more of aluminum nitride having a diameter of 5-50 nm.

The high-strength wire rod may have a prior austenite average grain size of 10 μm or smaller.

The martensite may be comprised of 60% or higher in the prior austenite grain boundary.

The present disclosure also provides a method for manufacturing a high-strength wire rod for cold heading with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics, which comprises: heating a billet comprising, by wt %, 0.3-0.6% of C, 0.05-0.3% of Si, 0.2-1.0% of Mn, 0.5-2.0% of Cr, 0.5-2.0% of Mo, 0.02-0.05% of Al, 0.01-0.03% of N and Fe and other impurities as the balance at 1000-1200° C., conducting hot rolling at a finish hot rolling temperature of 750-950° C., and conducting cooling at a cooling rate of 0.2-1.0° C./s, wherein the cooled wire rod has a microstructure comprising, by area fraction, 80% or more of bainite, 1-15% of pearlite and 0.1-2% of martensite, and comprises 2×1019/m3 or more of aluminum nitride having a diameter of 5-50 nm.

The present disclosure also provides a heat-treated component with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics, which comprises, by wt %, 0.3-0.6% of C, 0.05-0.3% of Si, 0.2-1.0% of Mn, 0.5-2.0% of Cr, 0.5-2.0% of Mo, 0.02-0.05% of Al, 0.01-0.03% of N and Fe and other impurities as the balance, and has a microstructure comprising, by area fraction, 90% or more of tempered martensite, and comprises 2×1019/m3 or more of aluminum nitride having a diameter of 5-50 nm.

The heat-treated component may have a prior austenite average grain size of 5 μm or smaller.

In addition, the heat-treated component with superior resistance of hydrogen-delayed fracture characteristics may have a tensile strength of 1400 MPa or higher and an impact toughness of 60 J or higher.

The present disclosure also provides a method for manufacturing a heat-treated component with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics, which comprises: preparing a wire rod comprising, by wt %, 0.3-0.6% of C, 0.05-0.3% of Si, 0.2-1.0% of Mn, 0.5-2.0% of Cr, 0.5-2.0% of Mo, 0.02-0.05% of Al, 0.01-0.03% of N and Fe and other impurities as the balance and having a microstructure comprising, by area fraction, 80% or more of bainite, 1-15% of pearlite and 0.1-2% of martensite, wherein the martensite is comprised of 60% or higher in the prior austenite grain into a steel wire by conducting spheroidization heat treatment and drawing once or more times, preparing the prepared steel wire into a component by conducting cold heading, heating the prepared component at 800-900° C. for 1,000-2,000 seconds, quenching the heated component at 50-150° C., and tempering the quenched component at 500-600° C. for 3,000-10,000 seconds.

Advantageous Effects

According to an exemplary embodiment of the present disclosure, since the microstructure comprises, by area fraction, 80% or more of bainite, 1-15% of pearlite and 0.1-2% of martensite, austenitization heat treatment can be conducted quickly and, thus, the energy consumed for heat treatment can be reduced.

According to an exemplary embodiment of the present disclosure, since the wire rod has a microstructure and fine carbide is distributed therein, resistance of hydrogen-delayed fracture resistance can be improved.

BRIEF DESCRIPTION OF DRAWINGS

FIG. 1 shows the tensile strength of examples and comparative examples.

FIG. 2 shows the impact toughness of examples and comparative examples.

 BEST MODE

The present specification discloses a high-strength wire rod for cold heading with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics, which comprises, by wt %, 0.3-0.6% of C, 0.05-0.3% of Si, 0.2-1.0% of Mn, 0.5-2.0% of Cr, 0.5-2.0% of Mo, 0.02-0.05% of Al, 0.01-0.03% of N and Fe and other impurities as the balance, and has a microstructure comprising, by area fraction, 80% or more of bainite, 1-15% of pearlite and 0.1-2% of martensite and comprises 2×1019/m3 or more of aluminum nitride having a diameter of 5-50 nm.

MODE FOR INVENTION

Hereinafter, specific exemplary embodiments of the present disclosure are described. However, the exemplary embodiments of the present disclosure may be modified in various forms and the technical idea of the present disclosure is not limited to the embodiments described below. In addition, the exemplary embodiments of the present disclosure are provided to more completely explain the present disclosure to those having ordinary knowledge in the art.

The terms used in this application are used only to describe specific examples. Therefore, for example, singular expressions include plural expressions unless the context clearly indicates otherwise. In addition, the terms such as “include”, “have”, etc. used in this application are used to clearly indicate that the features, steps, functions, components or combinations thereof described in the specification exist, but do not preclude the presence of other features, steps, functions, components or combinations thereof.

Meanwhile, unless defined otherwise, all the terms used in the present specification should be regarded as having the same meanings commonly understood by those having ordinary knowledge in the technical field to which the present disclosure belongs. Therefore, unless explicitly defined in the present specification, certain terms should not be interpreted in an overly idealistic or formal sense. For example, in the present specification, singular expressions include plural expressions unless the context clearly indicates otherwise.

In addition, the expressions such as “about”, “substantially”, etc. in the present specification are used to indicate specific or similar numerical values within given tolerances. They are used to help understanding the present disclosure or prevent undue exploitation of the disclosure by unscrupulous infringers.

A high-strength wire rod for cold heading with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics according to the present disclosure comprises, by wt %, 0.3-0.6% of C, 0.05-0.3% of Si, 0.2-1.0% of Mn, 0.5-2.0% of Cr, 0.5-2.0% of Mo, 0.02-0.05% of Al, 0.01-0.03% of N and Fe and other impurities as the balance.

The reason why the alloy composition is limited will be described in detail. The composition means wt % unless specified otherwise.

Carbon (C): 0.3-0.6 wt %

C is an element added to ensure the strength of a product. If the content of C is less than 0.3%, it is difficult to ensure the target strength, and it is not easy to ensure sufficient hardenability after final Q/T (quenching/tempering) heat treatment. On the contrary, if the content of C exceeds 0.6%, fatigue life is reduced due to excessive generation of carbide. Accordingly, in the present disclosure, the upper limit of the C content is limited to 0.6%.

Silicon (Si): 0.05-0.3 wt %

Si an element that is used not only for deoxidization of steel but also for ensuring strength through solid solution strengthening. In the present disclosure, Si is added in an amount of 0.05% or more for ensuring deoxidization and strength. But, if the content is excessive, it is difficult to process complex parts such as a bolt because of unsatisfactory cold heading property. Accordingly, in the present disclosure, the upper limit of the Si content is limited to 0.3%.

Manganese (Mn): 0.2-1.0 wt %

Mn is an element which is advantageous in ensuring strength by improving the hardenability of parts, increases rollability and reduces brittleness. It is added in an amount of 0.2% or more in order to ensure sufficient strength. But, if the content is excessive, a hard tissue may be formed easily during cooling after hot rolling and fatigue property may be deteriorated due to the generation a large amount of MnS inclusions. Accordingly, in the present disclosure, the upper limit of the Mn content is limited to 1.0%.

Chromium (Cr): 0.5-2.0 wt %

Cr is an element which is effective for improving hardenability together with Mn and improves the corrosion resistance. If the Cr content is less than 0.5%, enough corrosion resistance cannot be ensured. On the other hand, if the content is excessive, there are problems that impact toughness is decreased and coarse carbide with poor resistance of hydrogen-delayed fracture resistance is formed. Accordingly, in the present disclosure, the upper limit of the Cr content is limited to 2.0%.

Molybdenum (Mo): 0.5-2.0 wt %

Mo is an element which improves hardenability through precipitation hardening by precipitation of fine carbide and solid solution hardening. The improvement of hardenability by Mo is more effective as compared to Mn or Cr. If the Mo content is less than 0.5%, it is not easy to ensure strength because fine carbide is not precipitated sufficiently during Q/T heat treatment. On the other hand, if the content is excessive, the shape of the part is distorted after quenching due to excessively high hardenability, requiring an additional process for correction or resulting in microcrack defects in the parts. Accordingly, in the present disclosure, the upper limit of the Mo content is limited to 2.0%.

Aluminum (Al): 0.02-0.05 w %

Al is an element widely used as a deoxidizing agent in steelmaking processes. Al reacts with N to form aluminum nitride (AlN) and refines austenite grains. If the Al content is less than 0.02%, grain refinement is not easy because the amount of the nitrogen compound is insufficient. On the other hand, if the content is excessive, the occurrence of defects may be intensified due to excessive formation of non-metallic inclusions such as alumina. Accordingly, in the present disclosure, the upper limit of the Al content is limited to 0.05%.

Nitrogen (N): 0.01-0.03 w %

N is an element used for grain refinement instead of the expensive alloying element. N reacts with Al to form aluminum nitride (AlN) and refines austenite grains. If the content of N is less than 0.01%, grain refinement is not easy because the amount of the nitrogen compound is insufficient. On the other hand, if the content is excessive, dislocation and deposition occur during cold heading due to heading heat, resulting in decreased mold life due to fixation of free nitrogen and increased deformation strength. Accordingly, in the present disclosure, the upper limit of the N content is limited to 0.03%.

The remaining component is iron (Fe). But, the mixing of unwanted impurities from the raw materials or the surrounding environment cannot be excluded. The impurities will not be described in detail because they are known to those skilled in the art.

In addition, because coarse carbonitride strongly traps hydrogen and can cause hydrogen embrittlement, it is necessary to prevent its formation as much as possible. For reference, vanadium (V), which is frequently added to high-strength CHQ (cold heading quality) steel with a tensile strength of 1400 MPa or higher, can form coarse carbide having poor resistance of hydrogen-delayed fracture resistance. In the present disclosure, V is not added so that no undissolved coarse carbide remains after Q/T heat treatment even when a large part with a body diameter of 16-30 mm is manufactured. Through this, resistance of hydrogen-delayed fracture resistance can be ensured.

The wire rod for cold heading according to an exemplary embodiment of the present disclosure has a microstructure comprising, by area fraction, 80% or more of bainite, 1-15% of pearlite and 0.1-2% of martensite. When the wire rod has such a microstructure, the heat treatment time for dissolving cementite during austenitization heat treatment can be reduced.

In addition, the microstructure may contain 2×1019/m3 or more of aluminum nitride having a diameter of 5-50 nm and may have a prior austenite average grain size of 10 μm or smaller. When 2×1019/m3 or more of aluminum nitride having a diameter of 5-50 nm is comprised, austenite grains can be refined and resistance of hydrogen-delayed fracture resistance can be improved. Here, the prior austenite grain boundary of the wire rod refers to the grain boundary of the austenite structure of the wire rod after winding and before cooling.

In addition, 60% or more of martensite may be comprised in the prior austenite grain boundary. When 60% or more of martensite is comprised in the prior austenite grain boundary, a tensile strength of 1400 MPa or higher and an impact toughness of 60 J or higher can be ensured.

The inventors of the present disclosure have found out that the strength and resistance of hydrogen-delayed fracture resistance of the wire rod for cold heading can be improved further when the contents of C, Cr and Mo satisfy a specific condition, and have derived the following relation. In an exemplary embodiment of the present disclosure, the wire rod for cold heading may satisfy the following formula (1) while satisfying the above-described alloy composition.


7.2 C+Cr+2.7 Mo≥6.65  (1)

In the formula (1), C, Cr and Mo mean the wt % of each element. If there is an element other than C, Cr and Mo, 0 is allocated for the element.

In order to further improve resistance of hydrogen-delayed fracture resistance, fine carbide that can trap diffusible hydrogen is necessary. The fine carbides that can trap hydrogen comprise CrC and MoC carbides having Cr and Mo as main components, respectively. Only when a certain number of the fine carbides is ensured, a strength of 1400 MPa or higher can be ensured at the tempering temperature of 500-600° C. and the effect of hydrogen trapping can be maximized. Considering this, by controlling the alloy composition to satisfy the formula (1), the strength and resistance of hydrogen-delayed fracture resistance of the heat-treated component at the high tempering temperature (500-600° C.) can be improved.

Hereinafter, a method for manufacturing a high-strength wire rod for cold heading with superior resistance of hydrogen-delayed fracture characteristics according to the present disclosure will be described.

The method for manufacturing a high-strength wire rod for cold heading with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics according to an exemplary embodiment of the present disclosure may comprise a step of heating a billet satisfying the composition described above, a step of preparing the heated billet into a wire rod, and a step of cooling the wire rod.

In the step of heating the billet, the billet may satisfy the composition described above and may be heated at 1000-1200° C. In addition, the billet may satisfy the formula (1).

In the step of preparing the heated billet into a wire rod, the heated billet may be prepared into a wire rod by finish hot-rolling at 750-950° C. and then winding.

In the step of cooling the wire rod, the wire rod may be cooled at a cooling rate of 0.2-1.0° C./s such that the average austenite grain size after winding is 10 μm or smaller. The cooling may be performed by air cooling, although not being specially limited thereto.

The cooled wire rod may have a microstructure comprising, by area fraction, 80% or more of bainite, 1-15% of pearlite and 0.1-2% of martensite, and the aerial ratio of the martensite formed in the prior austenite grain boundary may be 60% or higher. Here, the prior austenite grain boundary refers to the grain boundary of the austenite structure of the wire rod after winding and before cooling. In addition, the microstructure of the cooled wire rod may contain 2×1019/m3 or more of aluminum nitride having a diameter of 5-50 nm.

Hereinafter, a method for manufacturing a high-strength heat-treated component with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics using the wire rod for cold heading described above will be described.

The method for manufacturing a high-strength heat-treated component with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics according to an exemplary embodiment of the present disclosure may comprise a step of lowering strength by spheroidization heat-treating the cooled wire rod, a step of preparing the wire rod into a component through cold heading, a step of heating the component, a step of quenching the heated component, and a step of tempering the quenched component. After the spheroidization heat treatment, drawing may be performed at least once. Hereinafter, each step will be described in detail.

The cooled wire rod may be prepared into a steel wire by conducting spheroidization heat treatment and drawing at least once. The spheroidization heat treatment is performed appropriately to process the steel before drawing, and the drawing may be performed appropriately in consideration of the drawing limit. According to the present disclosure, the wire rod may be prepared into a steel wire that can be prepared into a component of a complicated shape through spheroidization heat treatment and drawing.

The steel wire may be prepared into a component through cold heading. The component may be, for example, a screw, a bolt, etc. The bolt may have a body diameter of 12-30 mm.

Then, the component may be heated at high temperature. In the step of heating the component, the carbide precipitated during the rolling of the wire rod is redissolved. The component may be heated such that the alloy component has a uniform composition and has an average austenite grain size of 5 μm or smaller. In an exemplary embodiment, the component may be heated at 800-900° C. for 1000-2000 seconds.

In the step of quenching the heated component, the heated component may be quenched to 50-150° C. The quenching may be performed by immersing the heated component in an oil at 50-150° C., although not being specially limited thereto.

In the step of tempering the quenched component, the final microstructure of the heat-treated component is controlled to tempered martensite. In an exemplary embodiment, the tempering step may be performed by tempering at 500-600° C. The tempering may be performed for 3000-10000 seconds.

The heat-treated component with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics prepared by the method described above may contain, by wt %, 0.3-0.6% of C, 0.05-0.3% of Si, 0.2-1.0% of Mn, 0.5-2.0% of Cr, 0.5-2.0% of Mo, 0.02-0.05% of Al, 0.01-0.03% of N and Fe and other impurities as the balance, and the microstructure may contain, by area fraction, 90% or more of tempered martensite and may contain 2×1019/m3 or more of aluminum nitride having a diameter of 5-50 nm.

In addition, the prior austenite average grain size may be 5 μm or smaller. Here, the prior austenite grain boundary refers to the grain boundary of the austenite structure of the wire rod after winding and before cooling.

In addition, the tensile strength may be 1400 MPa or higher, and the impact toughness may be 60 J or higher. When the heat-treated component is a bolt, the final component with a body diameter of 12-30 mm may have a tensile strength of 1400 MPa or higher and an impact toughness of 60 J or higher.

In an exemplary embodiment of the present disclosure, the heat-treated component satisfying the alloy composition described above may satisfy the following formula (1). The restriction in the formula (1) will not be described here because it was described earlier.


7.2 C+Cr+2.7 Mo≥6.65  (1)

In the formula (1), C, Cr and Mo mean the wt % of each element.

Hereinafter, the present disclosure will be described more specifically through examples. However, the following examples are only for illustrating the present disclosure more specifically and the technical idea of the present disclosure is not limited by the examples.

EXAMPLES

A billet having the composition described in Table 1 was heated to 1000-1200° C., finish-rolled at 750-950° C., and then wound at 730-900° C. After the winding, the wire rod was cooled at a cooling rate of 0.2-1° C./s. After the cooling was completed, the wire rod had a microstructure comprising, by area fraction, 80% or more of bainite, 1-15% of pearlite and 0.1-2% of martensite, and the ratio of martensite formed in the prior austenite grain boundary was 60% or higher. In addition, it comprised 2×1019/m3 or more of aluminum nitride having a diameter of 5-50 nm.

In Table 1, ‘formula (1)’ was calculated by substituting the contents (wt %) of C, Cr and Mo in the ‘7.2 C+Cr+2.7 Mo’ of the formula (1). The AlN number indicates the number of aluminum nitride with a size of 5-50 nm.

TABLE 1 Grain AIN Alloy composition (wt %) Formula boundary number Division C Si Mn Cr Mo Al N (1) martensite ratio (%) (/m3) Example 1 0.32 0.11 0.71 1.23 1.19 0.04 0.015 6.747 63 4.3 × 1019 Example 2 0.41 0.11 0.62 1.01 1.12 0.03 0.016 6.986 62 3.4 × 1019 Example 3 0.56 0.12 0.82 0.81 0.92 0.03 0.016 7.326 64 3.6 × 1019 Example 4 0.42 0.10 0.72 1.52 0.95 0.03 0.017 7.109 63 5.0 × 1019 Example 5 0.40 0.11 0.56 0.57 1.45 0.03 0.014 7.365 70 3.1 × 1019 Comparative 0.32 0.13 0.69 1.25 0.85 0.03 0.016 5.849 65 3.6 × 1019 Example 1 Comparative 0.40 0.11 0.65 0.94 1.19 0.04 0.015 7.033 54 3.7 × 1019 Example 2 Comparative 0.54 0.11 0.75 0.83 0.94 0.03 0.009 7.256 68 1.9 × 1019 Example 3 Comparative 0.43 0.13 0.66 2.12 1.05 0.03 0.016 8.051 72 3.4 × 1019 Example 4 Comparative 0.41 0.10 0.76 0.77 2.21 0.04 0.015 9.689 74 3.7 × 1019 Example 5

For the examples, the values of the formula (1) were 6.65 or higher, the grain boundary martensite ratio was 60% or higher, and the number of aluminum nitride with a size of 5-50 nm was 2×1019/m3 or more.

In contrast, for the comparative examples, the values of the formula (1) were lower than 6.65, the grain boundary martensite ratio was lower than 60%, the number of aluminum nitride with a size of 5-50 nm was smaller than 2×1019/m3, or the alloy composition was outside the range of 0.3-0.6% of C, 0.05-0.3% of Si, 0.2-1.0% of Mn, 0.5-2.0% of Cr, 0.5-2.0% of Mo, 0.02-0.05% of Al and 0.01-0.03% of N.

The hot-rolled wire rod having the composition described in Table 1 was processed into a cylindrical sample with a diameter of 25 mm, heated at 860° C. for 1,500 seconds, quenched by immersing in an oil at 100° C., and then tempering at 500-600° C. for 5,000 seconds. Then, after processing into a test sample according to ASTM E8 and ASTM E23, tensile test and impact test were performed. The result of tensile test and impact test is shown in FIG. 1 and FIG. 2. All the examples exhibited a tensile strength of 1,400 MPa or higher and an impact toughness of 60 J or higher at the tempering temperature of 500-600° C., whereas the comparative examples showed poor tensile strength and impact toughness.

Although the exemplary embodiments of the present disclosure have been described above, the present disclosure is not limited thereto and those having ordinary knowledge in the art will understand that various changes and modifications can be made without departing from the concept and scope of the appended claims.

INDUSTRIAL APPLICABILITY

The present disclosure may provide a high-strength wire rod for cold heading with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics, a heat-treated component, and a method for manufacturing the same.

Claims

1. A high-strength wire rod for cold heading with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics, which comprises, by wt %, 0.3-0.6% of C, 0.05-0.3% of Si, 0.2-1.0% of Mn, 0.5-2.0% of Cr, 0.5-2.0% of Mo, 0.02-0.05% of Al, 0.01-0.03% of N, and Fe and other impurities as the balance, and has a microstructure comprising, by area fraction, 80% or more of bainite, 1-15% of pearlite and 0.1-2% of martensite, and comprises 2×1019/m3 or more of aluminum nitride having a diameter of 5-50 nm.

2. The high-strength wire rod for cold heading with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics according to claim 1, which has a prior austenite average grain size of 10 μm or smaller.

3. The high-strength wire rod for cold heading with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics according to claim 1, wherein the martensite is comprised of 60% or higher in the prior austenite grain boundary.

4. A method for manufacturing a high-strength wire rod for cold heading with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics, comprising:

heating a billet comprising, by wt %, 0.3-0.6% of C, 0.05-0.3% of Si, 0.2-1.0% of Mn, 0.5-2.0% of Cr, 0.5-2.0% of Mo, 0.02-0.05% of Al, 0.01-0.03% of N and Fe and other impurities as the balance at 1000-1200° C.,
hot rolling at a finish hot rolling temperature of 750-950° C., and
cooling at a cooling rate of 0.2-1.0° C./s,
wherein the cooled wire rod has a microstructure comprising, by area fraction, 80% or more of bainite, 1-15% of pearlite and 0.1-2% of martensite, and comprises 2×1019/m3 or more of aluminum nitride having a diameter of 5-50 nm.

5. A heat-treated component with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics, which comprises, by wt %, 0.3-0.6% of C, 0.05-0.3% of Si, 0.2-1.0% of Mn, 0.5-2.0% of Cr, 0.5-2.0% of Mo, 0.02-0.05% of Al, 0.01-0.03% of N and Fe and other impurities as the balance, and has a microstructure comprising, by area fraction, 90% or more of tempered martensite, and comprises 2×1019/m3 or more of aluminum nitride having a diameter of 5-50 nm.

6. The heat-treated component with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics according to claim 5, which has a prior austenite average grain size of 5 μm or smaller.

7. The heat-treated component with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics according to claim 5, which has a tensile strength of 1400 MPa or higher and an impact toughness of 60 J or higher.

8. A method for manufacturing a heat-treated component with superior heat treatment characteristics and resistance of hydrogen-delayed fracture characteristics, comprising:

preparing a wire rod comprising, by wt %, 0.3-0.6% of C, 0.05-0.3% of Si, 0.2-1.0% of Mn, 0.5-2.0% of Cr, 0.5-2.0% of Mo, 0.02-0.05% of Al, 0.01-0.03% of N and Fe and other impurities as the balance and having a microstructure comprising, by area fraction, 80% or more of bainite, 1-15% of pearlite and 0.1-2% of martensite, wherein the martensite is comprised of 60% or higher in the prior austenite grain boundary into a steel wire by conducting spheroidization heat treatment and drawing once or more times,
preparing the prepared steel wire into a component by conducting cold heading,
heating the prepared component at 800-900° C. for 1,000-2,000 seconds,
quenching the heated component at 50-150° C., and
tempering the quenched component at 500-600° C. for 3,000-10,000 seconds.
Patent History
Publication number: 20240052467
Type: Application
Filed: Nov 18, 2021
Publication Date: Feb 15, 2024
Applicant: POSCO CO., LTD (Pohang-si, Gyeongsangbuk-do)
Inventors: Byung-in JUNG (Pohang-si), Hanhwi KIM (Pohang-si, Gyeongsangbuk-do)
Application Number: 18/267,224
Classifications
International Classification: C22C 38/22 (20060101); C22C 38/02 (20060101); C22C 38/04 (20060101); C22C 38/06 (20060101); C22C 38/00 (20060101); C21D 8/06 (20060101); C21D 9/52 (20060101);