Patent Application
20240309500
This application is based on and claims the benefit of priority to Korean Patent Application No. 10-2020-0179748, filed on Dec. 21, 2020 in the Korean Intellectual Property Office, the disclosure of which is incorporated herein by reference.
The disclosure relates to an austenitic stainless steel with improved corrosion resistance and machinability and a manufacturing method the same, and more specifically, to an austenitic stainless steel with improved corrosion resistance and machinability for use in corrosive environments such as salt water and in an environment requiring machinability, and a manufacturing method the same.
Austenitic stainless steels used in mechanical parts such as frames, chambers, molds, and the like, are manufactured into final shapes by cutting processes such as milling. Machinability of stainless steels is required to reduce cutting load, increase cutting speed and improve tool life.
A type of steel to which Mn and S are added and uses MnS compounds which are a non-metallic inclusion is widely known as stainless steels with excellent machinability. However, MnS compounds readily elute in corrosive environments such as salt water or act as a starting point for pitting, which deteriorates the corrosion resistance of stainless steels. Therefore, stainless steels utilizing MnS compounds are limited in applications where corrosion resistance is required due to exposure to corrosive environments. Thus, stainless steels that are both machinable and corrosion resistant are required to be developed.
An aspect of the disclosure provides an austenitic stainless steel with improved corrosion resistance and machinability and a manufacturing method the same.
According to an embodiment of the disclosure, an austenitic stainless steel with improved corrosion resistance and machinability comprises, in percent by weight (wt %), 0.05% or less of C (excluding 0), 2% or less of Si (excluding 0), 2% or less of Mn (excluding 0), 0.01% or less of S, 16 to 22% of Cr, 9 to 15% of Ni, 3% or less of Mo (excluding 0), 0.15 to 0.25% of N, 0.004 to 0.06% of B, and the remainder being Fe and inevitable impurities. 10 or more BN precipitates are distributed per 100×100 μm2.
According to an embodiment of the disclosure, 10 or less MnS precipitates may be distributed per 100×100 μm2.
According to an embodiment of the disclosure, 10 or less MnS precipitates whose length of a major axis of 1 μm or more may be distributed per 100×100 μm2.
According to an embodiment of the disclosure, the austenitic stainless steel with improved corrosion resistance and machinability may further comprise, in percent by weight (wt %), 1% or less of Cu (excluding 0).
According to an embodiment of the disclosure, a pitting potential may be 300 mV or more.
According to an embodiment of the disclosure, a manufacturing method of an austenitic stainless steel with improved corrosion resistance and machinability may comprise: heating a stainless steel comprising, in percent by weight (wt %), 0.05% or less of C (excluding 0), 2% or less of Si (excluding 0), 2% or less of Mn (excluding 0), 0.01% or less of S, 16 to 22% of Cr, 9 to 15% of Ni, 3% or less of Mo (excluding 0), 0.15 to 0.25% of N, 0.004 to 0.06% of B, and the remainder being Fe and inevitable impurities at 1,150 to 1,250° C. for 1 hour and 30 minutes or more; hot rolling the heated stainless steel; and maintaining the hot-rolled steel at 1,100 to 1,250° C. for 30 seconds or more.
The present disclosure provides an austenitic stainless steel with improved corrosion resistance and machinability and a manufacturing method the same.
These and/or other aspects of the disclosure will become apparent and more readily appreciated from the following description of the embodiments, taken in conjunction with the accompanying drawings of which:
An austenitic stainless steel with improved corrosion resistance and machinability according to an embodiment of the present disclosure comprises, in percent by weight (wt %), 0.05% or less of C (excluding 0), 2% or less of Si (excluding 0), 2% or less of Mn (excluding 0), 0.01% or less of S, 16 to 22% of Cr, 9 to 15% of Ni, 3% or less of Mo (excluding 0), 0.15 to 0.25% of N, 0.004 to 0.06% of B, and the remainder being Fe and inevitable impurities, and 10 or more BN precipitates are distributed per 100×100 μm2.
This specification does not describe all the elements according to embodiments of the disclosure, and descriptions well-known in the art to which the disclosure pertains or overlapped portions are omitted.
Throughout the specification, the term “include” an element does not preclude other elements but may further include another element, unless otherwise stated.
As used herein, the singular forms are intended to include the plural forms as well, unless the context clearly dictates otherwise.
Hereinafter, embodiments of the disclosure will be described in detail.
The following embodiments of the present disclosure are provided to fully convey the spirit of the present disclosure to a person having ordinary skill in the art to which the present disclosure belongs. The present disclosure is not limited to the embodiments shown herein, but may be embodied in other forms.
According to the present disclosure, formation of MnS deteriorating corrosion resistance is excluded to prevent the formation of MnS precipitates. In addition, BN compounds are introduced to replace MnS to improve machinability.
However, addition of B in excess of an appropriate level causes fracture during hot rolling for producing a plate. Thus, the present inventors have found the optimized content of B, N and other elements to enable the formation of BN at an effective level for improving machinability while suppressing fracture during hot rolling.
According to an embodiment of the disclosure, the austenitic stainless steel with improved corrosion resistance and machinability comprises, in percent by weight (wt %), 0.05% or less of C (excluding 0), 2% or less of Si (excluding 0), 2% or less of Mn (excluding 0), 0.01% or less of S, 16 to 22% of Cr, 9 to 15% of Ni, 3% or less of Mo (excluding 0), 0.15 to 0.25% of N, 0.004 to 0.06% of B, and the remainder being Fe and inevitable impurities.
In addition, the austenitic stainless steel with improved corrosion resistance and machinability may further comprise, in percent by weight (wt %), 1% or less of Cu (excluding 0).
Hereinafter, reasons for numerical limitations on the contents of alloying elements in the embodiment of the present disclosure will be described. The unit is wt % unless otherwise stated.
The content of carbon (C) is 0.05% or less (excluding 0).
Carbon (C) is an austenite forming element and acts as an inevitable impurity. When the content of C exceeds 0.05%, the corrosion resistance of the welded part may be impaired, and thus the content of C is controlled to 0.05%.
The content of silicon (Si) is 2% or less (excluding 0).
Si is added as a deoxidizer and is an element for improving corrosion resistance. However, when the content of Si exceeds 2%, toughness may be deteriorated, and thus the Si content is controlled to 2% or less in the present disclosure.
The content of manganese (Mn) is 2% or less (excluding 0).
Mn is an austenite phase-stabilizing element. However, when the content of Mn exceeds 2%, corrosion resistance may be deteriorated, and thus the Mn content is controlled to 2% or less in the present disclosure.
The content of sulfur (S) is 0.01% or less.
The S content is controlled to 0.01% or less in order to prevent the formation of MnS to be excluded in the present disclosure.
The content of chromium (Cr) is from 16 to 22%.
Cr is an element for improving corrosion resistance of an austenitic stainless steel. When the Cr content is less than 16%, the above-described effect may not be obtained. The Cr content exceeding 22% may increase the raw material cost and decrease toughness. Therefore, the Cr content is controlled from 16 to 22% or less in the present disclosure.
The content of nickel (Ni) is from 9 to 15%.
Ni is an austenite phase-stabilizing element. When the Ni content is less than 9%, the above-described effect may not be obtained. The Ni content exceeding 15% causes an increase in raw material cost. Therefore, the Ni content is controlled from 9 to 15% or less in the present disclosure.
The content of molybdenum (Mo) is 3% or less (excluding 0).
Mo is an element for improving corrosion resistance. However, the Mo content exceeding 3% causes an increase in raw material cost, and thus the Mo content is controlled to 3% in the present disclosure.
The content of boron (B) is from 0.004 to 0.06%.
B is added to secure BN. When the content of B is less than 0.004%, sufficient BN targeted by the present disclosure may not be formed, and when the content of B exceeds 0.06%, fracture occurs during hot rolling. Therefore, the content of B is controlled to 0.004 to 0.06% in the present disclosure.
The content of nitrogen (N) is 0.15 to 0.25%.
N is added to secure BN. When the content of N is less than 0.15%, sufficient BN may not be formed, and when the content of N exceeds 0.25%, toughness is deteriorated. Therefore, the content of N is controlled to 0.15 to 0.25% in the present disclosure.
The content of copper (Cu) is 1% or less (excluding 0).
Cu is an element for improving corrosion resistance, and is added as required in the present disclosure. However, when the content of Cu exceeds 1%, hot workability may deteriorate, and thus the Cu content is controlled to 1% in the present disclosure.
The remaining component of the alloy composition of the present disclosure is iron (Fe). The austenitic stainless steel with improved corrosion resistance and machinability of the present disclosure may include other impurities that may be included in a typical industrial production process of steel. Since these impurities are known to those skilled in the art to which the present disclosure belongs, the type and content thereof are not specifically limited in the present disclosure.
In any section of the austenitic stainless steel according to the present disclosure, 10 or less MnS precipitates whose length of a major axis of 1 μm or more per 100×100 μm2 are distributed. In this instance, the MnS precipitate may comprise 50 at. % or more of the sum of Mn and S.
According to the present disclosure, since the formation of MnS causing deterioration of corrosion resistance is suppressed, corrosion resistance may be secured, and a pitting potential of the austenitic stainless steel of the present disclosure may be 300 mV or more.
In any section of the austenitic stainless steel according to the present disclosure, 10 or more BN precipitates per 100×100 μm2 are distributed. In this instance, the BN precipitates may comprise 50 at. % or more of the sum of B and N. According to the present disclosure, MnS is replaced with BN, thereby securing machinability while suppressing deterioration of corrosion resistance.
Next, a manufacturing method of austenitic stainless steel with improved corrosion resistance and machinability according to an embodiment of the present disclosure will be described.
The austenitic stainless steel with improved corrosion resistance and machinability according to an embodiment of the present disclosure may be manufactured in various methods, and the manufacturing method is not particularly limited. As an embodiment, however, the austenitic stainless steel with improved corrosion resistance and machinability according to an embodiment of the present disclosure may be manufactured as described below.
For example, the manufacturing method of austenitic stainless steel with improved corrosion resistance and machinability according to an embodiment of the present disclosure comprises, heating a stainless steel comprising, in percent by weight (wt %), 0.05% or less of C (excluding 0), 2% or less of Si (excluding 0), 2% or less of Mn (excluding 0), 0.01% or less of S, 16 to 22% of Cr, 9 to 15% of Ni, 3% or less of Mo (excluding 0), 0.15 to 0.25% of N, 0.004 to 0.06% of B, and the remainder being Fe and inevitable impurities, at 1,150 to 1,250° C. for 1 hour and 30 minutes or more; hot rolling the heated stainless steel; and maintaining the hot-rolled steel at 1,100 to 1,250° C. for 30 seconds or more.
In this instance, the heating is a process for forming as many BNs as possible, and may be performed at 1,150 to 1,250° C. for 1 hour and 30 minutes or more.
Also, the hot rolling may be performed up to a thickness of 8 mm, without being limited thereto, since the thickness may vary depending on the use.
In addition, the maintaining process after hot rolling is for forming BN again, and may be performed at 1,100 to 1,250° C. for 30 seconds or more.
Hereinafter, the present disclosure will be described in greater detail through examples. However, it is necessary to note that the following examples are only intended to illustrate the present disclosure in more detail and are not intended to limit the scope of the present disclosure. This is because the scope of the present disclosure is determined by matters described in the claims and able to be reasonably inferred therefrom.
An alloy satisfying the alloy composition of Table 1 was melt-cast, and the austenitic stainless steel cast was heated at 1,200° C. for 1 hour and 30 minutes. Thereafter, the heated steel cast was hot-rolled to become a thickness of 8 mm. Subsequently, the hot-rolled steel was maintained at a temperature of 1,150′ C for 30 seconds or more to form BN precipitates, thereby obtaining a hot-rolled steel specimen.
For the hot-rolled steel specimens of Examples 1 to 10 and Comparative Examples 1 to 7, whether fracture occurred after hot rolling was observed, and the case where fracture occurred was marked as 0, and the case where fracture did not occur was marked as X in Table 2 below.
Referring to Table 2, in Examples 1 to 10 satisfying the alloy composition of the present disclosure, no fracture occurred during hot rolling. However, in Comparative Example 2, the B content was satisfactory, but the N content did not reach the lower limit proposed in the present disclosure, resulting in fracture during hot rolling.
In Comparative Example 3, although the B content was satisfactory, the N content did not reach the lower limit proposed in the present disclosure, and thus fracture occurred during hot rolling.
Subsequently, for the hot-rolled steel specimens of Comparative Examples 1 and 4 to 6 and Examples 1 to 10, which were not fractured during hot rolling, BN precipitates and MnS precipitates were observed and corrosion resistance and machinability were evaluated, which are shown in Table 3 below.
BN precipitates and MnS precipitates were mirror-polished on an arbitrary cut surface of the steel plate, and then the number of MnS precipitates of 1 μm or more per 100×100 μm2 and the number of BN precipitates per 100×100 μm2 were observed using a Scanning Electron Microscope (SEM) to which an Energy Dispersive Spectrometer (EDS) is attached, and the numbers are shown.
Corrosion resistance was evaluated by pitting potential. The pitting potential is measured by immersing a hot-rolled steel specimen in an aqueous solution containing 3.5 wt % NaCl, connecting the electrodes, applying voltage, and measuring a voltage at the point where the current reaches 0.1 mA when the voltage was gradually raised from the natural potential.
Machinability was evaluated by measuring a cutting load torque under the conditions of cutting depth of 2 mm, cutting thickness of 5 mm, and end mill rotational speed of 2,000 rpm, when cutting using an end mill. However, since the cutting environment may change, the torque of Comparative Example 1 is used as a reference (100%).
Referring to Table 2 and Table 3, Examples 1 to 10 satisfying the alloy composition of the present disclosure do not form MnS precipitates, and thus corrosion resistance thereof are satisfactory with a pitting potential of more than 300 mV. Also, the cutting load is lower than that of Comparative Example 1, as the number of BN precipitates is more than 11 per 100×100 μm2, and thus it may be confirmed that machinability is also secured.
On the contrary, Comparative Example 1 shows satisfactory corrosion resistance with a pitting potential of 550 mV because MnS was not formed. However, BN was not formed because B was not added, and the cutting load was inferior to that of Examples.
In Comparative Example 4, MnS was formed and the cutting load was low, but the content of N did not reach the lower limit proposed in the present disclosure. Therefore, sufficient BN was not formed and corrosion resistance was inferior.
In Comparative Example 5, MnS was formed and the cutting load was low, but the B content and the N content did not reach the lower limit proposed in the present disclosure, and thus sufficient BN was not formed and corrosion resistance was inferior.
Comparative Example 6 shows satisfactory corrosion resistance with a pitting potential of 1000 mV because MnS was not formed. However, the cutting load was inferior because the content of B did not reach the lower limit proposed in the present disclosure.
Although embodiments have been described for illustrative purposes, those skilled in the art will appreciate that various modifications, additions and substitutions are possible, without departing from the scope and spirit of the disclosure. Therefore, embodiments have not been described for limiting purposes.
According to the present disclosure, provided are an austenitic stainless steel with improved corrosion resistance and machinability and a manufacturing method the same.
| Number | Date | Country | Kind |
|---|---|---|---|
| 10-2020-0179748 | Dec 2020 | KR | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/KR2021/018701 | 12/10/2021 | WO |
