Patent Application
20240052451
The present disclosure relates to a steel material for a seismic damper used to secure seismic resistance of a structure against an earthquake and a manufacturing method of the same.
In seismic design, which has been mainly used in Korea in the past, a technology of lowering a yield ratio of a steel material used in a structure of a column or beam during an earthquake to delay a point in time at which destruction of the structure occurs, was mainly used. However, the seismic design using such a steel material having a low yield ratio had a problem in that it is impossible to reuse the steel material used in the structure, and the structure itself should be reconstructed due to the absence of securing stability.
Recently, with the development of seismic design technology, a practical use of a seismic damping or vibration damping structure is progressing. In particular, various technologies for securing seismic performance by absorbing energy applied to a structure by an earthquake to a specific portion thereof are being developed. A seismic damper is used as a device for absorbing such seismic energy, and a steel material for a seismic damper has an ultra-low yield point characteristic. By lowering a yield point of the steel material for the seismic damper further than the existing structural material of a column or a beam, the steel material first yields during an earthquake to absorb vibration energy caused by the earthquake, and suppresses deformation of the structure by maintaining other structural materials within a range of elasticity.
However, the conventional steel material for the seismic damper utilizes ultra-low carbon steel to have a coarse ferrite structure, thereby exhibiting continuous yield behavior in which a yield point phenomenon is not exhibited during a tensile test. For this reason, while absorbing plastic strain energy generated by the earthquake, work hardening occurs rapidly, and the increase in yield strength is large, so there is a problem to be improved as a steel material for a damper for absorbing earthquake energy.
However, a technology at a level capable of meeting such high-end demand has not been developed so far.
An aspect of the present disclosure is to provide a steel sheet for a seismic damper, which has a low yield strength and can be used to secure seismic resistance of a structure against an earthquake and a manufacturing method of the same.
Alternatively, an aspect of the present disclosure is to provide a steel sheet for a seismic damper having a low yield strength and excellent low-temperature impact toughness simultaneously, and a manufacturing method of the same.
An object of the present disclosure is not limited to the above description. The object of the present disclosure will be understood from the entire content of the present specification, and a person skilled in the art to which the present disclosure pertains will understand an additional object of the present disclosure without difficulty.
According to an aspect of the present disclosure,
According to another aspect of the present disclosure, provided is a manufacturing method of a steel sheet for a seismic damper, the method including:
As set forth above, according to an aspect of the present disclosure, a steel sheet that can be suitably used for a seismic damper used to secure seismic resistance of a structure against an earthquake and a manufacturing method of the same may be provided.
Alternatively, according to another aspect of the present disclosure, a steel sheet for a seismic damper having a low yield strength and excellent low-temperature impact toughness and a manufacturing method of the same may be provided.
Various and beneficial merits and effects of the present disclosure are not limited to the descriptions above, and may be more easily understood in a process of describing specific exemplary embodiments in the present disclosure.
Hereinafter, preferred embodiments of the present disclosure will be described. However, embodiments of the present disclosure may be modified in various forms, and the scope of the present disclosure should not be construed as being limited to the embodiments described below. The present embodiments are provided to those skilled in the art to further elaborate the present disclosure.
As a steel material used to secure seismic resistance of a structure against an earthquake, conventionally, a technology of using a component close to pure iron and performing an additional heat treatment in a range of 910 to 960° C., has been known. However, since this technology requires performing an additional heat treatment at a high temperature of 900° C. or higher after finish rolling, excessive scale occurs in the case of a steel material having an ultra-low yield point to which Si is not added, so that defects occur, or coarse Nb or Ti precipitates are formed, so that there was a problem in that deterioration in impact toughness occurs. In addition, since an additional heat treatment process at a high temperature of 900° C. or higher is included, there is also a problem of causing an increase in manufacturing costs.
Alternatively, as a conventional steel material for a seismic damper, there has been a technology for controlling to have a coarse ferrite structure by utilizing ultra-low carbon steel, but this technology shows continuous yield behavior in which the yield point phenomenon does not occur during a tensile test. For this reason, work hardening occurs rapidly while absorbing plastic strain energy generated by an earthquake, resulting in a large increase in yield strength, so that there was a problem that needs to be improved as a steel sheet for a seismic damper for absorbing earthquake energy.
Accordingly, as a result of the examples thereof, the present inventors have developed a steel sheet for a seismic damper having a low yield strength and excellent low-temperature impact toughness, exhibiting a yield point phenomenon, resulting in completing a technology that can suppress an increase in yield strength by lowering rapid work hardening due to plastic deformation in the event of an earthquake.
Specifically, a steel sheet for a seismic damper according to an aspect of the present disclosure includes a base steel plate; and a scale layer formed on at least one surface of the base steel sheet.
In this case, the base steel sheet may include, by wt %, 0.005 to 0.02% of C, 0.05 to 0.2% of Si, 0.1 to 0.5% of Mn, 0.02% or less of P, 0.01% or less of S, 0.005 to 0.05% of Al, 0.005% or less of N, 0.02 to 0.06% of Nb, 48/14×[N] to 0.05% of Ti, with a balance of Fe and other unavoidable impurities.
Hereinafter, a reason for adding each alloy component constituting the composition of the base steel sheet, which is one of the main characteristics of the present invention, and an appropriate content range thereof will be first described.
C: 0.005 to 0.02%
C is an element causing solid solution strengthening and is fixed to dislocations in a free state to increase yield strength and decrease elongation. Therefore, in order to be suitably used as a steel material for a seismic damper, a C content needs to be controlled to 0.005% or more, and when the C content exceeds 0.02%, an appropriate strength for use as a seismic damper may be exceeded. Therefore, in the present disclosure, the C content is controlled to be 0.005 to 0.02%. However, more preferably, a lower limit of the C content may be 0.011%, or an upper limit of the C content may be 0.018%.
Si: 0.05 to 0.2%
Si, like C, is an element causing solid solution strengthening, and increases yield strength and lowers elongation, in order to be suitably used as a steel for a seismic damper, it is preferred to lower a Si content as much as possible. However, if Si is not added in an appropriate amount, adhesion of secondary scale generated during rolling is poor, so that the scale is formed on a surface of the steel sheet during production, increasing possibility of surface defects. Therefore, in the present disclosure, a Si content is controlled to 0.05% or more in terms of securing the adhesion of the secondary scale, and the Si content is controlled to 0.2% or less in terms of securing low yield strength. However, more preferably, a lower limit of the Si content may be 0.07%, or an upper limit of the Si content may be 0.15%.
Mn: 0.1 to 0.5%
Mn, like Si, is an element causing solid solution strengthening, to increase yield strength and lower elongation. Therefore, in order to be suitably used as a steel material for a seismic damper, in the present disclosure, a Mn content is controlled to 0.1% or more in terms of securing appropriate strength, and an upper limit thereof is controlled to 0.5% or less in order to avoid excessive solid solution strengthening effects. However, more preferably, a lower limit of the Mn content may be 0.18%, and the upper limit of the Mn content may be 0.35%.
P: 0.02% or Less (Excluding 0%)
P is an element that is advantageous for strength improvement and corrosion resistance, but it can greatly impair impact toughness, so it is preferable to maintain a P content to be as low as possible. Therefore, in the present disclosure, the P content may be controlled to 0.02% or less, more preferably 0.013% or less. In addition, as a lower limit of the P content, 0% may be excluded, considering an inevitably incorporated case, and more preferably, the lower limit of the P content may be 0.0005%.
S: 0.01% or Less (Excluding 0%)
Since S is an element that forms MnS, and the like to greatly impair impact toughness, it is preferable to keep an S content as low as possible. Therefore, in the present disclosure, the S content may be controlled to be 0.01% or less, more preferably 0.004% or less. In addition, as a lower limit of the S content, 0% may be excluded considering an inevitably incorporated case, and more preferably, the lower limit of the S content may be 0.0005% or more.
Al: 0.005 to 0.05%
Al is an element capable of inexpensively deoxidizing molten steel, and an upper limit of an Al content is controlled to 0.05% in terms of securing impact toughness while sufficiently lowering yield strength. Alternatively, more preferably, the upper limit of the Al content may be controlled to 0.035%, and a lower limit of the Al content may be controlled to 0.005% in terms of securing the minimum deoxidation performance. However, more preferably, the lower limit of the Al content may be 0.01%, and the upper limit of the Al content may be 0.035%.
N: 0.005% or Less (Excluding 0%)
N is an element causing solid solution strengthening and is fixed to dislocations in a free state to increase yield strength and decrease elongation. Therefore, the lower an N content, the better, so the N content is controlled to be 0.005% or less in terms of securing low yield strength. However, as a lower limit of the N content, 0% may be excluded considering an inevitably incorporated case, and more preferably, the lower limit of the N content may be 0.001% or more.
Nb: 0.02 to 0.06%
Nb is an important element in manufacturing TMCP steel, and is an element precipitated in a form of NbC or NbCN. In addition, Nb dissolved during reheating to a high temperature suppresses recrystallization of austenite, thereby exhibiting an effect of refining the structure.
Meanwhile, 0.02% or more of Nb is preferably added in order to promote desired deformation of organic precipitates. In addition, it is preferable to add Nb to 0.06% or less in order to prevent deterioration of impact toughness due to coarsening of precipitates. However, more preferably, a lower limit of the Nb content may be 0.03%, and an upper limit of the Nb content may be 0.05%.
Ti: 48/14×[N]˜0.05%
Ti is an element that serves to prevent N from being fixed to dislocations by precipitating in a form of TiN. Therefore, in order to adhere N in steel in an appropriate range, considering the added N content (weight %), Ti should be added in an amount of 48/14×[N]% or more, where [N] refers to a content (weight %) of N in the base steel sheet.
Meanwhile, when Ti is excessively added, there is a concern that impact toughness may deteriorate due to coarsening of precipitates, so Ti is controlled to 0.05% or less in terms of securing impact toughness. However, more preferably, a lower limit of the Ti content may be 0.02%, and an upper limit of the Ti content may be 0.045%.
Meanwhile, although not particularly limited, according to an aspect of the present disclosure, the base steel sheet satisfies the following Relational Expression 1.
0.001≤[C]−12/93×[Nb]−12/48×[A]≤0.01 [Relational Expression 1]
In Relational Expression 1, [C] represents an average content (weight %) of C in the base steel sheet, [Nb] represents an average content (weight %) of Nb in the base steel sheet, and [A] represents a value defined by the following Relational Expression 2.
[A]=[Ti]−48/12×[N] [Relational Expression 2]
In Relational Expression 2, [Ti] represents an average content (weight %) of Ti in the base steel sheet, and [N] represents an average content (weight %) of N in the base steel sheet.
According to an aspect of the present disclosure, a value of Free C expressed as [C]−12/93×[Nb]−12/48×[A] may be controlled in a range of 0.001 to 0.01%. When the value of Free C described above is less than 0.001%, it may be difficult that a yield point phenomenon is expressed, and the value thereof exceeds 0.01%, there is a risk of exceeding the appropriate strength that can be suitably used for the purpose of the seismic damper. That is, in the present disclosure, by satisfying the Relational Expression 1, it is possible to obtain a steel sheet in which excessive work hardening does not occur when an earthquake occurs by promoting the expression of an upper yield point.
Therefore, according to the present disclosure, it is possible to provide a steel sheet for a seismic damper having excellent low-temperature impact toughness, having a yield strength in a range of 205 to 245 MPa, a tensile strength of 300 MPa or more, and a Charpy impact transition temperature of −20° C. or lower.
In the present disclosure, remainder is Fe. However, since in the common manufacturing process, unintended impurities may be inevitably incorporated from raw materials or the surrounding environment, the component may not be excluded. Since these impurities are known to any person skilled in the common manufacturing process, the entire contents thereof are not particularly mentioned in the present specification.
According to an aspect of the present disclosure, the base steel sheet may include by area fraction, 95% or more (more preferably 99% or more) of ferrite as a microstructure, with a balance of 5% or less (including 0%) of other phases such as pearlite, or the like. Alternatively, most preferably, the base steel sheet has a single structure of ferrite (i.e., the base steel sheet includes, by area fraction, 100% of ferrite as a microstructure. By satisfying this, it is possible to effectively absorb energy when an earthquake occurs and serve as an earthquake damper.
In addition, although not particularly limited, according to an aspect of the present disclosure, in the base steel sheet, the average ferrite grain size may be in a range of 20 to 50 μm, more preferably 30 to 50 μm. In the base steel sheet, if the average ferrite grain size is less than 20 μm, a problem of exceeding a target yield strength may occur for use as a seismic damper. In the base steel sheet, when the average ferrite grain size exceeds 50 μm, dislocations can easily move due to the coarse ferrite grain size, resulting in a problem of exhibiting continuous yield behavior.
Based on a cutting surface of the steel material in the thickness direction (i.e., a direction perpendicular to a rolling direction), the average ferrite grain size described above refers to an average value of values obtained by measuring an equivalent circle diameter of the grains, and specifically, assuming that a spherical particle drawn with the longest length penetrating an inside of the grain as a particle diameter, the average ferrite grain size described above is an average value of the measured grain sizes.
Meanwhile, according to the present disclosure, a scale layer may be formed on at least one surface of the base steel sheet. In this case, although not particularly limited thereto, the scale layer may refer to a layer formed of FeO, Fe2SiO4, Fe2O3, Fe3O4, oxides of other alloying elements, and the like. depending on conditions in the manufacturing process of the steel sheet.
According to an aspect of the present disclosure, in the scale layer, a total content of FeO and Fe2SiO4 may be 2 to 5%, by wt %. When the total content of FeO and Fe2SiO4 is less than 2% by wt % with respect to the total content of the scale layer, the adhesion of the scale layer may deteriorate, resulting in irregular peeling of scale on the surface thereof. On the other hand, when the total content of FeO and Fe2SiO4 with respect to the total content of the scale layer exceeds 5%, the yield strength may exceed 245 MPa. In terms of further improving the effect described above, a lower limit of the total content of FeO and Fe2SiO4 with respect to the total content of the scale layer may be 2.28%, or the upper limit of the total content of FeO and Fe2SiO4 with respect to the total content of the scale layer may be 4%.
Meanwhile, although not particularly limited, according to an aspect of the present disclosure, in order to further improve the effect of providing the steel sheet for a seismic damper securing low yield strength and excellent low-temperature impact toughness and exhibiting the yield point phenomenon, and securing the adhesion of the scale layer to have excellent surface properties, the content of FeO in the scale layer may be 0.5 to 2%, by wt %, and/or the content of Fe2SiO4 in the scale layer may be 1 to 4.5%, by wt %. Alternatively, in terms of maximizing the effect described above, a lower limit of the content of FeO in the scale layer may be 0.79%, or an upper limit of the content of FeO in the scale layer may be 1.5%. Alternatively, in terms of maximizing the effect described above, a lower limit of the content of FeO in the scale layer may be 0.79%, or an upper limit of the content of FeO in the scale layer may be 1.5%.
In addition, according to an aspect of the present disclosure, a ratio (W1/W2) of a Fe2SiO4 content (W1) and a FeO content (W2) in the scale layer may be 1 to 9. In the scale layer, when the ratio of W1/W2 is less than 1.0, a problem of weakening adhesion of scale due to an insufficient ratio of Fe2SiO4 may occur, and when the ratio of W1/W2 exceeds 9, a problem of red scale may occur on the surface of the steel sheet. In terms of further improving effect described above, a lower limit of the ratio (W1/W2) may be 1.06, or an upper limit of the ratio (W1/W2) may be 4.
In addition, according to an aspect of the present disclosure, an average thickness of the scale layer may be 10 to 100 μm. When the average thickness of the scale layer is less than 10 μm, a problem of weakening the adhesion of the scale may occur, and when the average thickness exceeds 100 μm, a problem in processing may occur. Meanwhile, in order to further improve the effect described above, a lower limit of the average thickness of the scale layer may be 31 μm, or an upper limit of the average thickness of the scale layer may be 45 μm.
Hereinafter, a manufacturing method of a steel sheet for a seismic damper according to another aspect of the present disclosure will be described in detail. However, the manufacturing method of the steel sheet for a damper a seismic damper of the present disclosure does not necessarily mean that it must be manufactured by the following manufacturing method.
Slab Reheating Operation
A manufacturing method of a steel material for a seismic damper according to an aspect of the present disclosure may include an operation of reheating a steel slab satisfying the composition described above, wherein the reheating may be performed to a temperature within a range of 1050 to 1250° C. In this case, a heating temperature of the steel slab is controlled to be 1050° C. or higher in order to sufficiently dissolve a carbonitride of Ti and/or Nb formed during casting. However, when heated to an excessively high temperature, there may a concern of coarsening austenite, and it takes an excessive amount of time for a temperature of a surface thereof after rough rolling to reach a cooling start temperature of a surface layer portion, the slab may be preferably heated at 1250° C. or lower.
Descaling Operation after the Reheating Operation
When reheating the slab described above, oxides generated in a heating furnace may penetrate into a surface of the steel slab and deteriorate adhesion of a finally formed scale layer. Therefore, in order to improve surface quality through securing good adhesion of the scale layer, before a rough rolling operation after the reheating operation, high-pressure water having a pressure of 150 to 200 bars may be provided to the surface of the steel slab to perform a descaling treatment.
Rough Rolling Operation
According to an aspect of the present disclosure, before a finish rolling operation to be described later, the reheated steel slab may further include an operation of performing rough rolling to adjust a shape of the slab, and a temperature during rough rolling may be controlled to a temperature at which recrystallization of austenite stops (Tnr+50°) C or higher. It is possible to obtain an effect of destroying structural structures such as dentrite, or the like, formed during casting by rough rolling, and it is also possible to obtain an effect of reducing a size of austenite. Meanwhile, more preferably the rough rolling may be performed in a range of 999 to 1155° C.
Secondary Descaling Operation after the Rough Rolling Operation
Meanwhile, not only in the reheating operation of the slab described above, but also in the rough rolling operation, oxides formed on a surface of the rough-rolled bar may penetrate thereinto and affect adhesion of a finally-formed scale layer. Therefore, in the present disclosure, in order to improve surface quality through securing good adhesion of the scale layer, before a hot rolling operation after the rough rolling operation, high-pressure water having a pressure of 150 to bars may be selectively provided to a surface of the rough-rolled bar, to perform a descaling treatment, and the pressure of the high-pressure water in an operation of the secondary descaling treatment may be controlled to be within a range of 1 to 1.2 times the pressure of the high-pressure water in an operation of the primary descaling treatment. More preferably, the pressure may be controlled to be within a range of 1.02 to 1.2 times.
Hot Rolling Operation
The rough-rolled bar described above may be hot-rolled in a temperature range of Tnr or higher, and may be cooled by air cooling after the hot rolling.
When the hot rolling temperature is lower than Tnr, as illustrated in
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.
A steel slab having the alloy composition and properties illustrated in Table 1 below was prepared. In this case, a content of each component in Table 1 below is represented by wt %, and a balance thereof is Fe and inevitable impurities. That is, in the steel slabs described in Tables 1 and 2 below, Inventive Steels A to D illustrate an example matching a range of alloy compositions defined by the present disclosure, and Comparative Steels E to I illustrate an example deviating from the range of alloy compositions defined by the present disclosure.
After reheating the prepared steel slab in a temperature range of 1050 to 1250° C., slab reheating-rough rolling-hot rolling were performed under the conditions illustrated in Table 3 below to manufacture a steel material. In this case, before rough rolling after the reheating, high pressure water having a pressure of 150 bars was provided on a surface of the slab to perform a primary descaling treatment, and before hot rolling after the rough rolling, high pressure water having a pressure of 180 bars was provided on a surface of the rough-rolled bar to perform a secondary descaling treatment.
After manufacturing a steel sheet under the conditions described in Table 3 above, the steel sheet thus obtained was polishing-etched and then observed with an optical microscope. Therefore, it was confirmed that the base steel sheet has a ferrite single structure.
In addition, the results of measuring an average ferrite grain size, yield strength (YS), tensile strength (TS), and Charpy impact transition temperature of the steel sheet obtained from each Experimental Example were shown in Table 4 below. In this case, target ranges of the yield strength and tensile strength corresponding to the strength characteristic range desired in the present disclosure were shown in
In addition, an average thickness of the scale layer was measured by being imaged with an optical microscope to observe the scale layer, which was shown in Table 4 below. In addition, a content of FeO and Fe2SiO4 in the scale layer were measured using a scanning electron microscope and EDS, which was shown in Table 4 below.
In this case, the average ferrite grain size was measured using a line measurement method, and a point at which yielding occurs using a tensile tester was set to be a yield strength, and a strength when necking occurs was set to be tensile strength. For a Charpy impact transition temperature, an impact absorption energy was measured using a Charpy impact tester and a temperature at which fracture transitions from ductility to brittleness was shown.
Additionally, in order to evaluate surface properties of the steel sheet, a surface of the steel sheet having an area of 1 m2 was observed with a naked eye, and then a peeling area of the scale layer was measured and evaluated according to the following criteria.
As can be seen in Table 5, Examples satisfying both the steel composition and manufacturing conditions of the present disclosure, exhibited a yield point phenomenon and physical properties of the steel material had a yield strength of 205 to 245 MPa, tensile strength of 300 MPa or more, and Charpy impact transition temperature of −20° C. or lower.
In addition, in all the steel sheets obtained from the embodiments of the present disclosure, a total content of FeO and Fe2SiO4 in the scale layer satisfies a range of 2 to 5%, by wt %, and thereby, adhesion was excellent without peeling of the scale layer, so excellent surface properties were confirmed. It is determined that this is because SiO2 formed at a boundary between the scale and a base material reacts with FeO to form Fe2SiO4 (Fayalite), which increases binding force between the scale and the base material, resulting in a stable scale state.
In particular, with respect to the steel sheet obtained from Example 1-1, a photograph of a microstructure captured with an optical microscope is shown in
In addition, with respect to the steel sheet obtained from Example 1-1, after being manufactured so that a cross-section thereof in the thickness direction so that the scale layer can be observed, a photograph captured with an optical microscope was shown in
On the other hand, in Comparative Example 1, a C content was less than a lower limit specified in the present disclosure, and a value of Free C was insufficient, resulting in continuous yield, and the yield strength was less than 205 MPa.
In Comparative Example 2, the C content exceeded the content specified, so that the yield strength exceeded 245 MPa.
In Comparative Example 3, Si was added excessively, and the yield strength exceeded 245 MPa.
Comparative Example 4 showed a case in which the manufacturing conditions of the present disclosure are all satisfied, but a Ti content exceeded an upper limit specified in the present disclosure, and in Comparative Example 5, the Charpy impact transition temperature exceeded −20° C. due to the formation of coarse precipitates.
In Comparative Example 5, the yield strength was less than 205 MPa due to an insufficient Si content specified in the present disclosure, and a total content of FeO and Fe2SiO4 in the scale layer was less than 2%, by wt %, confirming that the surface properties were deteriorated. In particular, a state in which the scale layer is peeled for Comparative Example 5 was shown in
In addition, in the case of Reference Examples 1 to 4 satisfying the steel compositions of the present disclosure, but not satisfying the manufacturing conditions thereof, a case in which a hot rolling end temperature is less than Tnr was shown. In such Reference Examples 1 to 4, continuous yield behavior due to introduction of dislocations by rolling in a ferrite region, was shown and yield strengths all exceeded 245 MPa.
While example embodiments have been shown 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.
| Number | Date | Country | Kind |
|---|---|---|---|
| 10-2020-0179049 | Dec 2020 | KR | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/KR2021/017872 | 11/30/2021 | WO |
