Patent Application
20240253099
The invention relates to the field of steel rolling, particularly relates to a method for rolling high-toughness high-strength low-alloy steel (rolling method for a high-toughness high-strength low-alloy steel).
With the economic development of society and progress of science and technology, steel materials are already widely used in various fields, wherein, due to its high strength, good plasticity and toughness, a high-strength low-alloy steel is already widelyused in high-end fields such as aerospace and ships, especially in infrastructures such as oil pipes, bridges, large buildings, and engineering fields such as vehicles, containers, and machinery, chemical, medical, light industrial devices, it is also used broadly. The high-strength low-alloy steel is widely used in machinery devices, vehicles, and tubulation fields and so on due to its high strength, superior formability, and stable combination property.
At present, ways to increase strength of steel materials are solution strengthening, dislocation strengthening, refined crystalline strengthening, and precipitation hardening of a second-phase particle and so on; wherein, the effect of refined crystalline strengthening is most obvious, the steel after refined crystalline strengthening has better strength and toughness. With the increase of grain refinement resistance, crack propagation resistance, the fatigue strength, toughness of the steel increases, temperature of brittleness turning point decreases. A fine-grained steel has good coordination between strength and toughness, and is broadly used in fields such as vehicles, ships, bridges, and engineering machineries.
In prior art, there is a trade-off between strength and toughness of a high-strength low-alloy steel, the prior art only relates to a rolling method of a steel plate and strip, not relates to a rolling method of a round bar steel, and an off-line normalizing step is necessary during the rolling, production cost is high, which is adverse to energy saving in and cost reduction and green manufacturing.
With respect to deficiencies of the prior art, the purpose of the invention is to provide a rolling method for a high-toughness high-strength low-alloy steel. It successfully develops a rolling method for producing a high-toughness high-strength low-alloy steel by making a reasonable production process control through micro-alloy elements and control rolling and control cooling processes. During manufacturing of a production, it eliminates the off-line normalizing step, reduces the manufacturing process, saves manufacturing cost; for the high-strength low-alloy steel manufactured through this process and method, its metallographic structure is fine ferrite and pearlite, its tensile strength is more than 630 MPa, its yield strength is more than 500 MPa, its grain size after rolling is fine and uniform, the grain size reaches 9.0 or above, comprehensive mechanical properties are far superior to conventional rolling processes.
To achieve the above purpose, the invention provides the following technical solution:
A rolling method for high-toughness high-strength low-alloy steel, the rolling method sequentially comprises the following steps: heating, descaling, rough rolling, continuous rolling, first water cooling, finish rolling, second water cooling, and cold hearth cooling.
Using a converter continuous casting billet as a raw material, the continuous casting billet of the high-toughness high-strength low-alloy steel comprises the following chemical components and contents in percentage by mass: C≤0.20, Si≤0.60, Mn:1.37˜1.70, Cr≤0.30, P≤0.020, S≤0.020, V:0.05˜0.10, Al≤0.03, N≤0.025, with others being Fe and inevitable impurities.
In the above rolling method for high-toughness high-strength low-alloy steel, as a preferable embodiment, the step of the heating is divided into four sections, which are sequentially as follows: pre-heating zone, heating first zone, heating second zone, and soaking zone.
In the above rolling method for a high-toughness high-strength low-alloy steel, as a preferable embodiment, the temperature of the pre-heating zone is less than or equal to 750° C.
In the above rolling method for a high-toughness high-strength low-alloy steel, as a preferable embodiment, the temperature of the heating first zone is 900˜1050° C.
In the above rolling method for a high-toughness high-strength low-alloy steel, as a preferable embodiment, the temperature of the heating second zone is 1050˜1150° C.
In the above rolling method for a high-toughness high-strength low-alloy steel, as a preferable embodiment, the temperature of the soaking zone is 1150˜1210° C.
In the above rolling method for a high-toughness high-strength low-alloy steel, as a preferable embodiment, the total heating time of the step of the heating is 3˜5 h.
In the above rolling method for a high-toughness high-strength low-alloy steel, as a preferable embodiment, the soaking time of the soaking zone is 30˜80 min.
In the above rolling method for a high-toughness high-strength low-alloy steel, as a preferable embodiment, the step of the heating is performed in a four-section walking beam heating furnace.
In the above rolling method for a high-toughness high-strength low-alloy steel, as a preferable embodiment, in the step of the rough rolling, the entry temperature of the rough rolling is 950˜1050° C., the pass of the rough rolling is 5˜7, preferably, the number of rough-rolling mills provided in the step of the rough rolling is 6.
In the above rolling method for a high-toughness high-strength low-alloy steel, as a preferable embodiment, the step of the continuous rolling includes intermediate rolling and pre-finish rolling.
In the above rolling method for a high-toughness high-strength low-alloy steel, as a preferable embodiment, the entry temperature of the rough rolling is 900˜1000° C.
In the above rolling method for a high-toughness high-strength low-alloy steel, as a preferable embodiment, the number of intermediate-rolling mills provided in the step of the intermediate rolling is 6, the pass of the intermediate rolling is 5˜7, preferably, the pass of the intermediate rolling is 6.
In the above rolling method for a high-toughness high-strength low-alloy steel, as a preferable embodiment, outlet temperature of the pre-finish rolling is 850˜950° C.
In the above rolling method for a high-toughness high-strength low-alloy steel, as a preferable embodiment, the number of pre-finish-rolling mills provided in the step of the pre-finish rolling is 4, the pass of the pre-finish rolling is 3˜5, preferably, the pass of the pre-finish rolling is 4.
In the above rolling method for a high-toughness high-strength low-alloy steel, as a preferable embodiment, during the first water cooling, the first water cooling is performed with incoming materials after the step of the continuous rolling, wherein, the water cooling rate is 25˜50° C./s, the hydraulic pressure is 0.2˜0.6 MPa.
In the above rolling method for a high-toughness high-strength low-alloy steel, as a preferable embodiment, in the step of the finish rolling, rolling-start-temperature at the entry of the finish rolling is 800˜850° C.
In the above rolling method for a high-toughness high-strength low-alloy steel, as a preferable embodiment, a reducing and sizing mill set is used for the finish rolling.
In the above rolling method for a high-toughness high-strength low-alloy steel, as a preferable embodiment, the reducing and sizing mill set is a three-roller reducing and sizing mill set.
In the above rolling method for a high-toughness high-strength low-alloy steel, as a preferable embodiment, during the second water cooling, the second water cooling is performed with the steel after the step of the finish rolling, wherein, water cooling rate is 25˜100° C./s, hydraulic pressure is 0.2˜0.6 MPa.
In the above rolling method for a high-toughness high-strength low-alloy steel, as a preferable embodiment, in the step of the descaling, high-pressure water descaling is used with the aim to descaling, the hydraulic pressure of the high-pressure water is 15˜20 MPa.
Furthermore, preferably, the hydraulic pressure of the high-pressure water is 17˜20 MPa.
In the above rolling method for a high-toughness high-strength low-alloy steel, as a preferable embodiment, a high-toughness high-strength low-alloy steel bar is obtained by the rolling method, the specification of the steel bar is Ø60˜120 mm.
In the above rolling method for a high-toughness high-strength low-alloy steel, as a preferable embodiment, the cold hearth cooling means the steel after the second water cooling is cooled on the cold hearth.
Compared with the prior art, the beneficial effects of the invention are as follows:
At this point, applying the on-line TMCP process, controlling the precipitation process of nitrides, forming the ferrite and pearlite structure, grains are refined again by exploiting the low end rolling temperature and cooling rate. During the refinement of grains, the strength of the steel is improved, its plasticity and impact toughness are also enhanced, thus achieving high-strength control to mechanical properties.
The actual grain size of the high-strength low-alloy steel can be refined by adopting this rolling method, the comprehensive property of the obtained high-strength low-alloy steel is excellent, the metallographic structure is fine ferrite and pearlite, the tensile strength is more than 630 MPa, the yield strength is more than 500 MPa, the grain size after rolling is fine and uniform, the grain size reaches 9.0 or above, the impact energy at −20° C. is greater than 100 J, the impact energy at −40° C. is greater than 80 J, its comprehensive mechanical properties are far superior to conventional rolling processes.
The technical solutions of embodiments of the invention will be described clearly and fully in combination with drawings of embodiments of the invention below, obviously, the described embodiments are only some of the embodiments of the invention, not the all embodiments. Based on the embodiments of the invention, all the other embodiments obtained by those skilled in the art without doing any creative work will fall in the protection scope of the invention.
The rolling method disclosed in the invention results in a superior structural form and excellent structural mechanical properties of a necessary product by designing according to the process parameters of the continuous rolling, combining solid-state phase transformation and plastic deformation of the rolling principle, plastic forming through adopting the heating process system and the rolling reduction system of four-section stepwise heating furnace, forming through the deformation system of the rough rolling, the intermediate rolling, the finish rolling, finally controlling metal solid phase transformation through the cooling process.
The technical solution of the invention is further detailed in combination with drawings through the embodiments below.
A rolling method for a high-toughness high-strength low-alloy steel, the rolling method sequentially comprises the following steps: heating, descaling, rough rolling, continuous rolling, first water cooling, finish rolling, second water cooling, and cold hearth cooling; and using a converter continuous casting billet as a raw material, the continuous casting billet comprises the following chemical components and contents in percentage by mass: C≤0.20, Si≤0.60, Mn:1.00˜1.70, Cr≤0.30, P≤0.020, S≤0.020, V:0.05˜0.10, Al≤0.03, N≤0.025, with others being Fe and inevitable impurities.
By adding the micro-alloy element vanadium V into the chemical components of the continuous casting billet to improve hardenability of the steel, reduce steel deformation and cracks, and to enhance the impact toughness; because the micro-alloy element vanadium V has a delayed action on recrystallization only under 900° C., after austenitic transformation, the micro-alloy element vanadium V almost dissolves completely, the micro-alloy element N further enhances the impact toughnesses of micro-alloy elements at the same time, and precipitation strengthening effects of the micro-alloy element vanadium V, nitrogen N are exploited to the full.
The reason that grain refinement can improve plasticity and toughness is the fine grain provides a better condition for the occurrence and spread of plastic deformation. Elements those make temperature Ar3 decrease all have a tendency of grain refinement, temperature Ar3 causes austenite to transform into the ferrite. By adding the content of the micro-alloy element V to improve the impact toughness, at the meantime, it would have a strengthening effect when the micro-alloy element vanadium Vis dissolved into the ferrite, thus forming stable carbon compounds and refining grains.
The rolling method sequentially comprises the following steps:
The step of the heating is performed in a four-section stepwise heating furnace; the step of the heating is divided into four sections, which are sequentially as follows: pre-heating zone, heating first zone, heating second zone, and soaking zone.
The temperature of the pre-heating zone is less than or equal to 750° C. (for example. 600° C., 650° C., 665° C., 700° C., 750° C. and interval zones or points between any two of those temperatures); that is, if the temperature of the furnace exceeds 750° C., because thermal conductivity of the billet is too fast, the temperature difference between the billet and the heating furnace is too large, the surface of the casting billet or the final rolled steel may be caused to crack.
The temperature of the heating first zone is 900˜1050° C. (for example. 900° C., 950° C., 980° C., 1000° C., 1010° C., 1050° C. and interval zones or points between any two of those temperatures). The temperature of the heating second zone is 1050˜ 1150° C. (for example. 1050° C., 1080° C., 1100° C., 1110° C., 1130° C., 1150° C. and interval zones or points between any two of those temperatures). The main roles of the heating first zone and the heating second zone are to: reduce the energy consumption, reduce the oxidation burning loss of the billet.
The temperature of the soaking zone is 1150˜1210° C. (for example. 1150° C., 1160° C., 1165° C., 1170° C., 1185° C., 1190° C., 1205° C., 1210° C. and interval zones or points between any two of those temperatures). The main role of the soaking heating section is to: reduce the energy consumption, reduce the oxidation burning loss of the billet, reduce the decarburization of the billet at the same time.
The total heating time of the step of the heating is 3˜5 h (for example. 3.5 h, 4 h, 4.5 h, 4.8 h and time points between any two of those times); the soaking time of the soaking zone is 30˜80 min (for example. 30 min, 35 min, 40 min, 45 min, 50 min, 55 min, 60 min, 70 min, 75 min, 80 min and time points between any two of those time periods).
The step of the heating achieves the following four purposes: firstly, the energy consumption may be reduced and the cost can be lowed when eliminating the step of the off-line normalizing; secondly, the oxidation burning loss of the billet can be reduced due to the four-zoneheating process; thirdly, the decarburization of the billet can be reduced; fourthly, the surface cracks of the final billet brought by too long heating time can be reduced.
The billet after heating is descaled by employing the high-pressure water in order to deoxidate the iron sheet, the pressure of the high-pressure water is 15˜20 MPa (for example 15 MPa, 16.5 MPa, 17 MPa, 18 MPa, 20 MPa and the pressure value between any two of those pressure values); the pressure value of the high-pressure water is preferably 17˜20 MPa. The oxidized iron sheet on the surface of the steel is removed by the high-pressure water. The oxidized iron sheet on the surface cannot be cleared cleanly and thoroughly when the pressure is below 15 MPa, thus affecting the rolling effect of the steel.
Preferably, 6 rough rolling mills are provided in the step of the rough rolling; wherein, the entry temperature of the rough rolling is 950˜1050° C. (for example, 950° C., 980° C., 1000° C., 1020° C., 1035° C., 1050° C. and interval zones or points between any two of those temperatures), the pass of the rough rolling is 5˜7; the pass of the rough rolling is preferably 6. A method of continuous rolling is adopted in the step of the rough rolling, the surface size of the steel billet is changed mainly through plastic deformation, the pass design adopts a box pass design, the sectional shape of the billet is changed and reduced through the high-pressure process.
The step of the continuous rolling includes intermediate rolling and pre-finish rolling, the entry temperature of the intermediate rolling is 900˜1000° C. (for example, 905° C., 920° C., 940° C., 950° C., 970° C., 1000° C. and interval zones or points between any two of those temperatures), 6 intermediate rolling mills are preferably provided in the step of the intermediate rolling, the pass of the intermediate rolling is 5˜7, the pass of the intermediate rolling is preferably 6. The pass design mainly adopts an oval and circle pass design, the sectional shape of the billet is made close to the finished form through the rolling process.
The outlet temperature of the pre-finish rolling is 850˜950° C. (for example, 855° C., 870° C., 890° C., 900° C., 910° C., 920° C., 930° C., 940° C., 950° C. and interval zones or points between any two of those temperatures); 4 pre-finish rolling mills are preferably provided in the step of the pre-finish rolling, the pass of the pre-finish rolling is 3˜5, the pass of the pre-finish rolling is preferably 4. The pass design mainly adopts an oval and circle pass design, the sectional shape of the billet is made close to the finished form through the rolling process.
The first water cooling is performed with incoming materials after the step of the continuous rolling, the temperature after the first water cooling is 750˜800° C. (for example, 750° C., 765° C., 780° C., 795° C., 798° C., 800° C. and interval zones or points between any two of those temperatures), wherein, during the first water cooling, the water cooling rate is 25˜50° C./s, the hydraulic pressure is 0.2˜0.6 MPa. The target temperature as required in the finish rolling is obtained by controlling the temperature of the first water cooling and the water cooling rate, controlling the temperature of the steel before the pre-finish rolling.
The rolled steel obtained in the step (5) is rolled in a reducing and sizing finish rolling mill set, the reducing and sizing finish rolling mill set is preferably a three-roller reducing and sizing mill set, i.e. KOCKS reducing and sizing finish rolling mill set, entry temperature of initial rolling is 800˜850° C. (for example, 800° C., 810° C., 820° C., 824° C., 832° C., 850° C. and interval zones or points between any two of those temperatures). Adopting the three-roller reducing and sizing mill set can achieve low-temperature rolling better, thus improving non-quenched and tempered steel grain size, comprehensive mechanical properties, providing its excellent performance for the production of the non-quenched and tempered steel.
The second water cooling is performed with the steel after the finish rolling, the temperature under which the steel performs the second water cooling after the step of the finish rolling is 600˜700° C. (for example, 600° C., 625° C., 640° C., 662° C., 683° C., 700° C. and interval zones or points between any two of those temperatures), wherein, the water cooling rate is 25˜100° C./s, the hydraulic pressure is 0.2˜0.6 MPa. The metallographic structure and mechanical properties as finally required by the steel are obtained by performing the second water cooling after the finish rolling and controlling the temperature and the water cooling rate of the second water cooling, and controlling the temperature of the steel.
The steel obtained after the second water cooling is made to cool on the cold hearth, the finish steel is finally obtained.
The technology of controlling rolling and controlling cooling as described in the step (1) to the step (8) is the main steps of refining the grain size of the high-carbon steel grade, by integrally controlling the heating temperature, deformation extent, and cooling rate, the target of refining the actual grain size, improving stiffness and roughness of the steel is reached.
At the same time, applying the on-line TMCP process (i.e. thermal mechanical control process), controlling the precipitation process of nitrides, forming the uniform ferrite and pearlite structure, grains are refined again by exploiting the low end rolling temperature and cooling rate, during the refinement of grains, the strength of the steel is improved, its plasticity and impact toughness are also enhanced, thus achieving high-strength control to mechanical properties.
The invention provides a rolling method for a high-toughness high-strength low-alloy steel, this method is unique, adopts the micro-alloy elements and the control rolling and control cooling technology of the thermal mechanical control process to act collectively so as to implement the on-line control, adopting this process method can refine the actual grain size of the high-toughness high-strength low-alloy steel, the comprehensive performance of the high-strength low-alloy steel is excellent; the metallographic structure is fine ferrite and pearlite, the tensile strength is more than 630 MPa, the yield strength is more than 500 MPa, the grain size after rolling is fine and uniform, the grain size reaches 9.0 or above, Charpy V impact energy at −20° C. is greater than 100 J, and Charpy V impact energy at −40° C. is greater than 80 J, its comprehensive mechanical properties are far superior to conventional rolling methods. The high-toughness high-strength low-alloy steel is not performing the off-line normalizing during the manufacturing, the mechanical properties also can meet the request for utilization, this can not only save the machining time, but also can reduce the cost and improve the effect.
Embodiment 1 provides a rolling method for a high-toughness high-strength low-alloy steel, the specification of the required finished form is Ø65 mm, and 300×400 mm sectional continuous casting billet is selected; wherein, the continuous casting billet comprises the chemical components in percentage by mass, as shown in Table 2, the mass percentage is totally 100%, comprising the following steps:
The hot-rolled structure of the high-toughness high-strength low-alloy steel obtained in embodiment 1 is a uniform ferrite and pearlite, the actual grain size is 9.0, its mechanical properties of the steel product are as shown in Table 3. The hot-rolled structure of the high-toughness high-strength low-alloy steel obtained in embodiment 1 is a uniform ferrite and pearlite, the actual grain size is 9.0, as seen from Table 3, its mechanical properties of the steel product are excellent.
Embodiment 2 provides a rolling method for a high-toughness high-strength low-alloy steel, the specification of the required finished form is Ø80 mm, and 300×400 mm sectional continuous casting billet is selected; wherein, the continuous casting billet comprises the chemical components in percentage by mass, as shown in Table 2, the mass percentage is totally 100%; the rolling method sequentially comprises the following steps: (1) heating, (2) descaling, (3) rough rolling, (4) continuous rolling, (5) first water cooling, (6) finish rolling, (7) second water cooling, and (8) cold hearth cooled (cold hearth cooling), the processing step of example 2 is the same as that of example 1, see Table 1 for its processing parameters of specific steps, its mechanical properties of the steel product are as shown in Table 3.
The hot-rolled structure of the high-toughness high-strength low-alloy steel obtained in example 2 is a uniform ferrite and pearlite, as shown in
Embodiment 3 provides a rolling method for a high-toughness high-strength low-alloy steel, the specification of the required finished form is Ø100 mm; and 300×400 mm sectional continuous casting billet is selected; wherein, the continuous casting billet comprises the chemical components in percentage by mass, as shown in Table 2, the mass percentage is totally 100%; the rolling method sequentially comprises the following steps: (1) heating, (2) descaling, (3) rough rolling, (4) continuous rolling, (5) first water cooling, (6) finish rolling, (7) second water cooling, and (8) cold hearth cooled (cold hearth cooling), the processing step of embodiment 3 is the same as that of embodiment 1, see Table 1 for its processing parameters of specific steps, its mechanical properties of the steel product are as shown in Table 3.
The hot-rolled structure of the high-toughness high-strength low-alloy steel obtained in embodiment 3 is a uniform ferrite and pearlite, the actual grain size is 9.0, as shown in
The specific parameters of the processing step in embodiments 1-3 is shown in Table 1.
Chemical components of the continuous casting billet selected and used in embodiments 1-3 are shown in Table 2.
Each property of the high-toughness high-strength low-alloy steel obtained in embodiments 1-3 is shown in Table 3.
Embodiments 4-7 provide a rolling method for a high-toughness high-strength low-alloy steel, the rolling method sequentially comprises the following steps: (1) heating, (2) descaling, (3) rough rolling, (4) continuous rolling, (5) first water cooling, (6) finish rolling, (7) second water cooling, and (8) cold hearth cooled (cold hearth cooling), the processing step and the mechanical parameters of embodiments 4-7 are the same as those of embodiment 1; the continuous casting billet of embodiments 4-7 comprises the chemical components in percentage by mass, as shown in Table 4, the mass percentage is totally 100%.
Each property of the high-toughness high-strength low-alloy steel obtained in embodiments 4-7 is shown in Table 5.
As known from Table 5, the hot-rolled structure of the high-toughness high-strength low-alloy steel obtained in embodiments 4-7 is a uniform ferrite and pearlite, the actual grain size is 9.0, its mechanical properties of the steel product are excellent.
The specification of the required finished form is Ø65 mm, select 300×400 mm sectional continuous casting billet; the chemical components and contents of the continuous casting billet are: C0.45, Si 0.28, Mn1.46, Cr 0.16, V0.06, N0.010, Al 0.020, P≤0.020, S≤0.020, with the balance being Fe and inevitable impurities. The processing step and parameters of the alloy steel are shown in
As shown in Table 6, because the content of carbon C in the chemical components of the continuous casting billet is 0.45%, i.e. C>0.20, as shown in Table 8, the ductility of the rolled steel is 18%, Charpy V impact energy at −20° C. is 32 J; Charpy V impact energy at −40° C. is 17 J.
The specification of the required finished form is Ø80 mm, select 300×400 mm sectional continuous casting billet; the chemical components and contents of the continuous casting billet are: C0.16, Si 0.30, Mn 0.8, Cr 0.15, V0.07, N0.012, Al 0.020, P≤0.020, S≤0.020, with the balance being Fe and inevitable impurities. The processing step and parameters of the alloy steel are shown in
As shown in Table 6, because the content of manganese Mn in the chemical components of the continuous casting billet is 0.8, i.e. Mn<1.0, as shown in Table 8, the ductility of the rolled steel is 26%, Charpy V impact energy at −20° C. is 54 J; Charpy V impact energy at −40° C. is 25 J.
The specification of the required finished form is Ø100 mm, select 300×400 mm sectional continuous casting billet; the chemical components and contents of the continuous casting billet are: C0.16, Si 0.30, Mn 1.40, Cr 0.15, N0.011, Al 0.022, P≤0.020, S≤0.020, with the balance being Fe and inevitable impurities. The processing step and parameters of the alloy steel are shown in
As shown in Table 6, because vanadium V is not added into the chemical components of the continuous casting billet, as shown in Table 8, the ductility of the rolled steel is 25%, Charpy V impact energy at −20° C. is 35 J; Charpy V impact energy at −40° C. is 19 J.
The specification of the required finished form is Ø90 mm, select 300×400 mm sectional continuous casting billet; the chemical components and contents of the continuous casting billet are: C0.16, Si 0.32, Mn 1.47, Cr 0.15, V0.06, N0.040, Al 0.020, P≤0.020, S≤0.020, with the balance being Fe and inevitable impurities. The processing step and parameters of the alloy steel are shown in
As shown in Table 6, because the content of nitrogen N in the chemical components of the continuous casting billet is 0.040, i.e. N>0.025, as shown in Table 8, the ductility of the rolled steel is 27%, Charpy V impact energy at −20° C. is 62 J; Charpy V impact energy at −40° C. is 37 J.
As known from Table 8, through comparison the rolling method of the comparative examples 1-4 with that disclosed in the application, for the mechanical properties of the obtained steel, Charpy V impact energies at −20° C. are all less than 100 J, Charpy V impact energies at −40° C. are less than 80 J, the grain sizes of the alloy steel after rolling do not reach 9.0 or above.
The processing step and parameters of the alloy steel in comparative examples 1-4 are as shown in Table 7.
Each property of the alloy steel obtained in comparative examples 1-4 are shown in Table 8.
Although preferable examples of the invention are already described, the technical engineering person in the art may make other changes and modifications to those examples. Therefore, the attached claims should be interpreted as including preferable examples and all changes and modifications falling in the scope of the invention.
The above contents are only preferable examples of the invention, and not limited to the invention, for those skilled in the art, the invention may have various changes and varieties. Any changes, equivalent substitutions, improvements that are made within the spirit and principle of the invention should be included in the protection scope.
| Number | Date | Country | Kind |
|---|---|---|---|
| 202110519204.6 | May 2021 | CN | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/CN2022/092306 | 5/11/2022 | WO |
