KR101828713B1 - Steel reinforcement and method of manufacturing the same - Google Patents

Abstract

In one embodiment, the method of making reinforcing bars comprises 0.1 to 1.5 wt% carbon (C), 0.05 to 1.0 wt% silicon (Si), 0.5 to 16.0 wt% manganese (Mn) (Al) 0 to 9.0% by weight, Cr (Cr) 0.2 to 4.0% by weight, Ni (Ni) 0.1 to 0.5% by weight, 0.03 wt.% To 0.5 wt.% Of a total of one or more of nitrogen (N), 0.005 wt.% To 0.015 wt.%, Titanium niobium (Nb) and vanadium (V), and the balance iron and unavoidable impurities Lt; RTI ID = 0.0 > 1200 C < / RTI >; Hot-rolling the reheated billet to an Ac1 to 1000 占 폚 finish rolling temperature; Cooling the hot-rolled steel to a temperature of Ms-100 (占 폚) to Ms (占 폚) via a temp core; And recovering the cooled steel at 500 ° C to 600 ° C; .

Description

TECHNICAL FIELD [0001] The present invention relates to a reinforcing bar and a method of manufacturing the reinforcing bar.

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a reinforcing bar and a manufacturing method thereof, and more particularly to a lightweight reinforcing bar having high strength and high ductility, and a manufacturing method thereof.

Generally, carbon steel has an advantage that it is cheap and the material control by heat treatment is easy. As an example, carbon steel has been applied throughout the industry such as automobiles and machine parts. These carbon steels are also applied to structures for securing space for human activities. As an example, steel for structures has been widely applied to skyscrapers, long bridges, giant marine structures, underground structures, and the like.

On the other hand, the carbon steel can be applied to various industries in the form of reinforcing bars. As an example, in the case of reinforcing bars applied to a structure, it is required that the structure has a high strength and a high ductility while maintaining a relatively light weight as the superstructure and the gigantic structure.

A background art related to the present invention is Korean Patent Laid-Open Publication No. 10-2014-0041279.

The present invention provides a lightweight reinforcing bar having high strength and high ductility through alloy components and process control.

An embodiment of the present invention is a method of manufacturing a semiconductor device comprising 0.1 to 1.5% by weight of carbon (C), 0.05 to 1.0% by weight of silicon (Si), 0.5 to 16.0% by weight of manganese (Mn) (S) 0 to 0.03 wt%, Al (Al) 0 to 9.0 wt%, Cr (Cr) 0.2 to 4.0 wt%, Ni (Ni) 0.1 to 0.5 wt%, nitrogen ), 0.003 to 0.5% by weight of a total of at least one of titanium (Ti), niobium (Nb) and vanadium (V), and the balance iron (Fe) and unavoidable impurities. Reheating the billet having a temperature of 1100 DEG C to 1200 DEG C; Hot-rolling the reheated billet to an Ac1 to 1000 占 폚 finish rolling temperature; Cooling the hot-rolled steel to a temperature of Ms-100 (占 폚) to Ms (占 폚) via a temp core; And recovering the cooled steel at 500 ° C to 600 ° C; The present invention relates to a method of manufacturing a reinforcing bar including a reinforcing bar.

Another embodiment of the present invention is a process for the production of silicon carbide from 0.1 wt% to 1.5 wt% carbon (C), from 0.05 wt% to 1.0 wt% silicon (Si), from 0.5 wt% to 16.0 wt% manganese (Mn) (S) 0 to 0.03 wt%, Al (Al) 0 to 9.0 wt%, Cr (Cr) 0.2 to 4.0 wt%, Ni (Ni) 0.1 to 0.5 wt%, nitrogen ), 0.003 to 0.5% by weight of a total of at least one of titanium (Ti), niobium (Nb) and vanadium (V), and the balance iron (Fe) and unavoidable impurities. (TS) of 1100 MPa or more, and a tensile strength x elongation (TS x EL) of 20000 MPa ·% or more.

The reinforcing bar may have a specific gravity of 6.5 gm ^-3 to 7.0 gm ^-3 .

The reinforcing bars may include Fe ₂ AlC fine particles having an average particle diameter of 10 nm to 100 nm in a dispersed state.

The reinforcing bars may have a composite structure of ferrite, austenite, and kappa (?) - carbide.

According to the present invention, it is possible to provide a lightweight reinforcing bar having high strength and high ductility by uniformly forming Fe3AlC fine grain particles in the matrix metal through dispersion strengthening.

1 shows a method of manufacturing a reinforcing bar of the present invention.
2 shows the microstructure of the rebar produced in Example 1 of the present invention.
3 shows the microstructure of the rebar produced in Example 3 of the present invention.
4 shows the microstructure of the rebar produced in Comparative Example 1 of the present invention.

An embodiment of the present invention is a method of manufacturing a semiconductor device comprising 0.1 to 1.5% by weight of carbon (C), 0.05 to 1.0% by weight of silicon (Si), 0.5 to 16.0% by weight of manganese (Mn) (S) 0 to 0.03 wt%, Al (Al) 0 to 9.0 wt%, Cr (Cr) 0.2 to 4.0 wt%, Ni (Ni) 0.1 to 0.5 wt%, nitrogen ), 0.003 to 0.5% by weight of a total of at least one of titanium (Ti), niobium (Nb) and vanadium (V), and the balance iron (Fe) and unavoidable impurities. Reheating the billet having a temperature of 1100 DEG C to 1200 DEG C; Hot-rolling the reheated billet to an Ac1 to 1000 占 폚 finish rolling temperature; Cooling the hot-rolled steel through a temp core to a surface temperature of Ms-100 to Ms (占 폚); And recovering the cooled steel at 500 ° C to 600 ° C; The present invention relates to a method of manufacturing a reinforcing bar including a reinforcing bar. As a result, it is possible to provide a lightweight reinforcing bar having high strength and high ductility by a dispersion strengthening method in which Fe3AlC fine grain particles are uniformly formed in a matrix metal.

Another embodiment of the present invention is a process for the production of silicon carbide from 0.1 wt% to 1.5 wt% carbon (C), from 0.05 wt% to 1.0 wt% silicon (Si), from 0.5 wt% to 16.0 wt% manganese (Mn) (S) 0 to 0.03 wt%, Al (Al) 0 to 9.0 wt%, Cr (Cr) 0.2 to 4.0 wt%, Ni (Ni) 0.1 to 0.5 wt%, nitrogen ), 0.003 to 0.5% by weight of a total of at least one of titanium (Ti), niobium (Nb) and vanadium (V), and the balance iron (Fe) and unavoidable impurities. (TS) of 1100 MPa or more, and a tensile strength x elongation (TS x EL) of 20000 MPa ·% or more. Such reinforcing bars are achieved by the above-described method of producing reinforcing bars.

The reinforcing bars may include Fe ₂ AlC fine particles having an average particle diameter of 10 nm to 100 nm in a dispersed state.

The steel may have a specific gravity of from 6.5 gm ^-3 to 7.0 gm ^-3 .

The reinforcing bars may have a composite structure of ferrite, austenite, and kappa (?) - carbide.

Hereinafter, the role and content of each component contained in the reinforcing bar according to the present invention will be described.

Carbon (C)

In the present invention, carbon (C) is added to secure strength and hardness of the steel. Carbon (C) is dissolved in austenite to form martensite structure during quenching. In addition, the quenching hardness is improved as the amount of carbon is increased, and the possibility of deformation during quenching may increase.

The carbon (C) is added in an amount of 0.1 wt% to 1.5 wt% of the total weight. When the content of carbon is less than 0.1% by weight, it is difficult to secure sufficient strength. On the other hand, when the content of carbon (C) exceeds 1.5% by weight, the strength of the steel increases, but the core hardness decreases, the sufficient elongation is hardly secured, and the percentage of pearlite phase in the microstructure increases.

silicon( Si )

In the present invention, silicon (Si) is added as a deoxidizer to remove oxygen in the steel in the steelmaking process. Further, silicon (Si) is effective for improving the toughness and ductility of steel by inducing ferrite formation as a ferrite stabilizing element having a solid solution strengthening effect. Silicon (Si) also has the effect of increasing the softening constant at all when tempered.

The silicon (Si) is added in an amount of 0.05 wt% to 1.0 wt% of the total weight. When the content of silicon (Si) is less than 0.05% by weight, the effect of adding silicon can not be exhibited properly. On the contrary, when the content of silicon (Si) exceeds 1.0% by weight, oxides are formed on the surface of the steel to deteriorate ductility and toughness of the steel.

Manganese (Mn)

Manganese (Mn) is a substitutional element having an atomic diameter similar to iron. It increases the strength and toughness of the steel and increases the incombustibility of the steel, while lowering the ductility when the strength is increased as compared with the addition of carbon (C). Manganese (Mn) is an element highly effective in solid solution strengthening and contributes to improvement of hardenability of steel, and improves hardenability of steel.

The manganese (Mn) is added in an amount of 0.5 wt% to 16.0 wt% of the total weight. When the content of manganese (Mn) is less than 0.5% by weight, improvement in yield strength due to solid solution strengthening of ferrite may not be sufficient. On the contrary, when the content of manganese (Mn) exceeds 16% by weight, the amount of MnS-based nonmetal inclusions increases, which may lead to defects such as cracking during casting, quenching cracking or deformation, And the possibility that cold microstructure is expressed in the final tissue is increased.

In (P)

Phosphorus (P) is an element that contributes a little to the strength improvement, but if it is included excessively, the ductility of the steel is deteriorated and the final material deviation is caused by billet center segregation. P is not a problem if it is uniformly distributed in the steel, but usually forms harmful compounds of Fe3P. This Fe3P is extremely weak and is segregated and is not homogenized even after annealing, and it is elongated when it is forged or rolled.

The phosphorus (P) is limited to a content of more than 0 to 0.03% by weight of the total weight. When the content of phosphorus (P) is more than 0.03% by weight, not only center segregation but also fine segregation is formed, which adversely affects the material and may deteriorate ductility and toughness.

Sulfur (S)

Sulfur (S) is an element which contributes partly to the improvement of workability. However, if it is included excessively, sulfur (S) inhibits toughness and ductility of steel and forms MnS nonmetallic inclusion by binding with manganese. Sulfur can combine with iron to form FeS if the amount of manganese in the steel is insufficient.

The sulfur (S) is limited to an amount of more than 0 to 0.03% by weight of the total weight. When the content of sulfur (S) exceeds 0.03% by weight, there is a problem that ductility is greatly deteriorated and MnS non-metallic inclusions are excessively generated.

Aluminum (Al)

Aluminum (Al) acts as a deoxidizer to remove oxygen in the steel. Al is generally used as a deoxidizer. However, in this patent, in order to maximize the effect of reducing the specific gravity of the steel itself, up to 9 wt% is added to increase the lattice constant and replace the Fe atoms. The addition of about 7.5% wt has a 10% reduction in specific gravity.

The aluminum (Al) is added in an amount of 0 to 9.0 wt% of the total weight. If the content of aluminum (Al) exceeds 9.0 wt%, Al ₂ O ₃ is formed to deteriorate toughness.

chrome( Cr )

Chromium (Cr) is an effective element added to secure strength, which can improve the hardenability of steel and improve the strength by bonding with carbon to form carbides. It is possible to form a homogeneous oxide film on the surface of the plate material to reduce the decarburization part of the surface layer of the plate material.

Cr (Cr) is added in an amount of 0.2 wt% to 4.0 wt% of the total weight. If the content of chromium (Cr) is less than 0.2 wt%, it may be difficult to secure the strength even if the content of carbon (C) is high. On the other hand, when the content of chromium (Cr) exceeds 4.0% by weight, there is a problem that the ductility and the heat affected zone (HAZ) toughness are lowered.

nickel( Ni )

Nickel (Ni) is refined in grains and dissolved in austenite and ferrite to strengthen the matrix and improve the hardenability. In particular, nickel (Ni) is an element effective for promoting the formation of low-temperature phase microstructure and improving low-temperature impact toughness. Coexisting with chrome or molybdenum shows excellent hardenability, facilitates heat treatment of large steel, and forms austenitic stainless steel and heat resistant steel in combination with chromium because it is an austenite stabilizing element. It strengthens low temperature toughness of steel and does not harm weldability and malleability. Since the diffusion of carbon and nitrogen is slowed, the deterioration of the heat resistant steel is prevented, and the expansion rate, rigidity and porosity are improved.

The nickel (Ni) is added in an amount of 0.1 wt% to 0.5 wt% of the total weight of the steel sheet according to the present invention. When the content of nickel (Ni) is less than 0.1 wt%, it may be difficult to exhibit the effect of adding nickel (Ni) properly. On the contrary, when the content of nickel (Ni) is more than 0.5% by weight and added in a large amount, it may cause redispersibility brittleness.

Nitrogen (N)

Nitrogen (N) is an inevitable impurity, and there is a problem that inclusions such as AlN and TiN are formed and the quality of the steel is deteriorated. Nitrogen is added in an amount of 0.005 wt% to 0.015 wt%.

If the content of nitrogen (N) is less than 0.005% by weight, the nitrogen content must be controlled to a very small amount, which leads to an increase in the manufacturing cost and difficulties in management. On the contrary, when the content of nitrogen (N) exceeds 0.015% by weight, the amount of solute nitrogen is increased, which deteriorates the impact characteristics and elongation of the steel and greatly deteriorates the toughness of the welded portion.

titanium( Ti ), Naubium ( Nb ), And vanadium (V)

The alloy composition may further include at least one of titanium (Ti) niobium (Nb) and vanadium (V) in a total amount of 0.03 wt% to 0.5 wt%.

In the present invention, titanium (Ti) forms a carbide upon reheating to inhibit the growth of austenite grains, to refine the steel texture and increase the strength. The ability to form carbides of Ti, V, and Nb is stronger than chromium and makes crystal grains finer, so it is also used for the improvement of stainless steels and cutting tool steels. It is also used with precipitated hardened steel and permanent magnets because of its remarkable precipitation hardening effect by forming compounds with other metal elements.

The titanium (Ti) may be added in an amount of 0.03 wt% to 0.5 wt% of the total weight. If the content of titanium (Ti) is less than 0.03% by weight, the effect of adding titanium can not be exhibited properly. On the other hand, when the content of titanium (Ti) exceeds 0.5% by weight, carbonized precipitates become coarse, the effect of suppressing crystal grain growth is deteriorated, and it is difficult to secure ductility.

Niobium (Nb) combines with carbon (C) and nitrogen (N) at high temperatures to form carbides or nitrides. Niobium-based carbides or nitrides improve grain strength and low-temperature toughness by suppressing grain growth during rolling and making crystal grains finer.

The niobium (Nb) is added in an amount of 0.03 wt% to 0.5 wt% of the total weight. If the content of niobium (Nb) is less than 0.03% by weight, the effect of adding niobium can not be exhibited properly. On the contrary, when the content of niobium (Nb) exceeds 0.5% by weight, the ductility of the steel is lowered. The strength and the low temperature toughness due to the increase of the niobium content are not improved any more, but are present in a solid state in the ferrite, There is a risk of degradation.

Vanadium (V) combines with carbon (C) and nitrogen (N) at high temperatures to form carbides or nitrides. In addition, vanadium (V) plays a role in improving the strength of steel through precipitation strengthening effect by precipitate formation.

The vanadium is added in an amount of 0.03 wt% to 0.5 wt% of the total weight. If the content of vanadium is less than 0.03% by weight, it may be difficult to exhibit the effect of adding vanadium properly. On the contrary, if the addition amount of vanadium exceeds 0.5% by weight, it may be a factor to lower the impact resistance at low temperature.

In addition to the components of the alloy composition described above, the remainder is composed of iron (Fe) and impurities inevitably included in the steelmaking process and the like.

Method of manufacturing reinforcing bars

1 is a flowchart schematically showing a method of manufacturing a reinforcing bar according to an embodiment of the present invention. Referring to FIG. 1, the method for manufacturing the reinforcing bars includes a reheating step S100, a hot rolling step S200, a cooling step S300, and a repetition step S400. At this time, the reheating step (S100) is not necessarily performed, but is carried out in order to obtain effects such as reuse of precipitates.

In the method of manufacturing a reinforcing bar according to the present invention, the semi-finished steel to be subjected to the hot rolling process has the above-described alloy composition. The semi-finished steel may be, for example, a billet.

Reheating

In the reheating step (S100), the billet having the above-described alloy composition is reheated to 1100 to 1200 占 폚. The steel having the alloy composition may be obtained through a continuous casting process after obtaining a molten steel having a desired composition through a steelmaking process. By reheating these steels, segregated components can be reused in casting.

In the reheating step (S100), when the reheating temperature is less than 1100 DEG C, the segregated components are not sufficiently reused in the casting, and a rolling load is caused in the hot rolling. Further, titanium in the alloy component is not sufficiently re-used, so that coarsening of the precipitate occurs and it is difficult to secure sufficient strength. On the contrary, when the reheating temperature is higher than 1200 ° C, the austenite grain size increases and the strength can not be ensured, and the steel manufacturing cost can be increased due to the excessive heating process.

Hot rolling

In the hot rolling step (S200), the reheated steel is hot-rolled to a finish rolling temperature of Ac1 to 1000 占 폚. In this case, the crystal grains can be refined due to repetition of recovery and recrystallization during rolling.

When the finishing rolling temperature (FRT) is less than Ac1, it is difficult to ensure the workability of the steel sheet due to the occurrence of a complicated structure due to the rolling of the abnormal region, which may cause a load in the rolling process. On the other hand, when the finishing rolling temperature (FRT) is higher than 1000 ° C, the quality of the steel sheet due to the surface scale of the steel sheet is lowered, and the grain size due to the hot rolling is increased.

The finish rolling temperature (FRT) in the hot rolling step (S200) may be, for example, 850 to 1000 ° C.

Cooling

In the cooling step S300, the surface of the hot-rolled steel is cooled to a temperature of Ms-100 (占 폚) to Ms (占 폚) via the core of the temp. The effect of suppressing the growth of coarser crystal grains in the cooling temperature range is excellent.

Double heat

In step S400, the cooled rolled material is reheated to 500 to 600 ° C. It is possible to secure a microstructure having ferrite, austenite and kappa (-) - carbide in the above-mentioned double temperature range. When the double refraction temperature is less than 550 캜, it is difficult to secure the workability due to the increase in strength and the decrease in ductility due to grain refinement. On the other hand, when the coiling temperature exceeds 600 캜, ductility is secured but the strength is lowered.

The reinforcing bars according to the embodiment of the present invention can be manufactured by proceeding with the processes including the steps S100 to S400. According to the embodiment of the present invention, it is possible to provide a lightweight reinforcing bar having high strength and high ductility through dispersion strengthening that uniformly forms Fe3AlC fine grain particles in the base metal. As an example, a reinforcing bar according to an embodiment of the present invention may have a tensile strength (TS) of at least 1100 MPa and a tensile strength x elongation (TS EL) value of at least 20000 MPa.

Example

Hereinafter, the configuration and operation of the present invention will be described in more detail with reference to preferred embodiments of the present invention. It is to be understood, however, that the same is by way of illustration and example only and is not to be construed in a limiting sense.

The contents not described here are sufficiently technically inferior to those skilled in the art, and a description thereof will be omitted.

1. Preparation of specimens

A billet consisting of the alloy composition shown in Table 1 and the remaining iron (Fe) and unavoidable impurities was prepared.

The billets were hot-rolled under the conditions shown in Table 2 below to prepare specimens of Examples 1 to 3 and Comparative Examples 1 and 2.

division
Chemical composition (% by weight) importance
C Si Mn S P Al Cr Ni Nb Ti V Cu N Example 1 0.79 0.25 13.06 0.005 0.02 6.28 2.29 0.1 - 0.02 0.03 - 0.0120 6.98 Example 2 1.18 0.24 13.25 0.004 0.02 7.97 2.24 0.11 0.02 - 0.04 - 0.0111 6.93 Example 3 1.19 0.24 13.19 0.005 0.02 7.88 4.59 0.11 0.02 - 0.04 - 0.0130 6.91 Comparative Example 1 0.35 0.25 1.4 0.005 0.03 0.01 0.2 0.1 - - 0.05 0.2 0.0080 7.89 Comparative Example 2 0.25 0.20 20.0 0.005 0.02 10.0 - 0.10 - - - - - 6.94

division
Rolling conditions (캜) Reheating final Double heat Example 1 1200 970 520 Example 2 1200 973 516 Example 3 1200 965 526 Comparative Example 1 1030 930 570 Comparative Example 2 1200 900 570

2. Property evaluation

Table 3 shows the results of evaluation of mechanical properties of the specimens prepared according to Examples 1 to 3 and Comparative Examples 1 and 2. The physical properties were evaluated by measuring tensile strength (TS), yield strength (YS) and elongation (EL).

division YS (MPa) TS (MPa) EL (%) TS * EL (MPa 占%) Microstructure Example 1 992 1,133 24.8 28098.4 α + γ + κ Example 2 1,185 1,285 29 37265 α + γ + κ Example 3 1,094 1,179 19.8 23344.2 α + γ + κ Comparative Example 1 651 832 14.3 11897.6 α + Fe ₃ C Comparative Example 2 600 770 10.1 7,777 γ + κ

Referring to Table 3, in the case of the specimens according to Examples of the present invention, the tensile strength (TS) of 1100 MPa or more were all satisfied. In the case of Examples 1 to 3, both tensile strength x elongation (TS x EL) of 20000 MPa.% Or more were satisfied. Particularly, in the case of the specimen of Example 2, the tensile strength (TS) is 1200 MPa or more, and the tensile strength x elongation (TS x EL) is 35000 MPa ·% or more.

The specimens of Comparative Examples 1 and 2 had a tensile strength (TS) of less than 1000 MPa and a tensile strength x elongation (TS EL) of less than 20000 MPa.%.

 2 to 4 are photographs of microstructural sections of the specimens of Example 2, Example 3 and Comparative Example 1, respectively.

The specimens of Examples 2 and 3 exhibited a composite structure of ferrite, austenite and kappa-carbide. In the specimen of Comparative Example 1, composite structure of ferrite and cementite was shown.

While the invention has been described in connection with what is presently considered to be the most practical and preferred embodiment, it is to be understood that the invention is not limited to the disclosed embodiments. Such changes and modifications are intended to fall within the scope of the present invention unless they depart from the scope of the present invention. Accordingly, the scope of the present invention should be determined by the following claims.

S100 reheat step
S200 Step of hot rolling
S300 Cooling step
Step S400

Claims (8)

(P) more than 0 and 0.03% by weight, sulfur (S), silicon (Si), silicon (Si) 0 to 0.03 wt%, Al (Al) 0 to 9.0 wt%, Cr (Cr) 0.2 wt% to 4.0 wt%, Ni (Ni) 0.1 wt% to 0.5 wt%, N (0.005 wt% (Ti), niobium (Nb) and vanadium (V) in an amount of 0.03 wt% to 0.5 wt%, and the balance of iron (Fe) and unavoidable impurities, ≪ / RTI >
Hot-rolling the reheated billet to an Ac1 to 1000 占 폚 finish rolling temperature;
Cooling the hot-rolled steel to a temperature of Ms-100 (占 폚) to Ms (占 폚) via a temp core; And
Heating the cooled steel at 500 ° C to 600 ° C; , ≪ / RTI &
(TS) of 1100 MPa or more, tensile strength x elongation (TS x EL) of 20000 MPa ·% or more
Method of manufacturing reinforcing bars.
delete The method according to claim 1,
The produced reinforcing bars
And Fe ₂ AlC fine grain particles having an average particle diameter of 10 nm to 100 nm in a dispersed state.
The method according to claim 1,
Wherein the produced reinforcing bar has a composite structure of ferrite, austenite, and kappa-carbide.
(P) more than 0 and 0.03% by weight, sulfur (S), silicon (Si), silicon (Si) 0 to 0.03 wt%, Al (Al) 0 to 9.0 wt%, Cr (Cr) 0.2 wt% to 4.0 wt%, Ni (Ni) 0.1 wt% to 0.5 wt%, N (0.005 wt% 0.03 to 0.5% by weight of a total of at least one of titanium (Ti), niobium (Nb) and vanadium (V) and an alloy composition comprising the balance of iron (Fe) and unavoidable impurities, 1100 MPa or more, and tensile strength x elongation (TS x EL) 20000 MPa ·% or more.
6. The method of claim 5,
Wherein the reinforcing bars comprise Fe ₂ AlC fine grain particles having an average particle size of 10 nm to 100 nm in a dispersed state.
6. The method of claim 5,
Wherein the reinforcing bar has a specific gravity of 6.5 gm ^-3 to 7.0 gm ^-3
rebar.
6. The method of claim 5,
The reinforcing bar is a reinforcing bar having a composite structure of ferrite, austenite, and kappa (?) - carbide.

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