CN115725900B - High-strength high-plasticity bainitic steel and production method thereof - Google Patents
High-strength high-plasticity bainitic steel and production method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 52
- 239000010959 steel Substances 0.000 title claims abstract description 52
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 21
- 238000001816 cooling Methods 0.000 claims abstract description 45
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 36
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 34
- 238000005096 rolling process Methods 0.000 claims abstract description 21
- 230000009466 transformation Effects 0.000 claims abstract description 17
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 6
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 6
- 239000000126 substance Substances 0.000 claims abstract description 6
- 238000000034 method Methods 0.000 claims description 20
- 238000010438 heat treatment Methods 0.000 claims description 11
- 230000007704 transition Effects 0.000 claims description 9
- 229910000734 martensite Inorganic materials 0.000 claims description 7
- 238000005098 hot rolling Methods 0.000 claims description 4
- 230000009467 reduction Effects 0.000 claims description 4
- 239000012535 impurity Substances 0.000 claims description 2
- 229910045601 alloy Inorganic materials 0.000 abstract description 7
- 239000000956 alloy Substances 0.000 abstract description 7
- 238000002360 preparation method Methods 0.000 abstract description 6
- 229910052799 carbon Inorganic materials 0.000 description 11
- 230000008569 process Effects 0.000 description 11
- 230000000717 retained effect Effects 0.000 description 11
- 239000000463 material Substances 0.000 description 10
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 9
- 239000011572 manganese Substances 0.000 description 8
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 6
- 230000000052 comparative effect Effects 0.000 description 6
- 238000011160 research Methods 0.000 description 5
- 229910000797 Ultra-high-strength steel Inorganic materials 0.000 description 4
- 238000011161 development Methods 0.000 description 4
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 3
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 3
- 238000005265 energy consumption Methods 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 3
- 229910052710 silicon Inorganic materials 0.000 description 3
- 239000010703 silicon Substances 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 229910001567 cementite Inorganic materials 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 238000010276 construction Methods 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 230000005764 inhibitory process Effects 0.000 description 2
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 229910020012 Nb—Ti Inorganic materials 0.000 description 1
- 238000003723 Smelting Methods 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000001627 detrimental effect Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 238000011056 performance test Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000002035 prolonged effect Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000012827 research and development Methods 0.000 description 1
- 238000004904 shortening Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 239000002699 waste material Substances 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
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- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
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Abstract
A high-strength high-plasticity bainitic steel comprises the following chemical components in percentage by weight: c:0.35 to 0.65 percent, si:1.72 to 2.12 percent of Mn:2.30 to 2.55 percent of Al: 0.30 to 0.57 percent; the production method comprises the following steps: austenitizing the hot rolled sheet; first cooling; first-pass high-temperature rolling pre-deformation; cooling for the second time; rolling and deforming for the second time; cooling for the third time; air-cooling to room temperature. The alloy element is the most basic element, the cost is low, the production process is simple, the preparation period is short, no additional equipment is needed, and the preparation process is environment-friendly; the yield strength of the prepared ultra-high strength bainitic steel is 1392-1435 MPa, the tensile strength is 1771-1900 MPa, the elongation is 16.6-19.2%, and the strength-plastic product is 31.0-34.58%; the structure is thinned through austenite pre-deformation, the bainite transformation is accelerated, the stability of residual austenite is improved, and the comprehensive mechanical properties of the bainite steel are effectively improved.
Description
Technical Field
The invention belongs to bainitic steel for engineering machinery and a production method thereof. In particular to a high-strength high-plasticity bainitic steel for engineering machinery and a production method thereof.
Background
Along with the development trend of high specification in the steel market, the service performance of the product is promoted to be continuously updated so as to meet the higher requirements of the market on steel materials, and the ultra-high strength steel product becomes a research and innovation hot spot gradually and is also valued by the steel research and enterprise industry. However, it is known that as the strength level of steel increases, the plasticity and toughness thereof decrease.
Under the development trend of ultrahigh strength of steel materials, maintaining good plasticity and toughness is an important problem faced by steel materials. The aim of the development of new generation of steel materials is to have good elongation while satisfying ultra-high strength. Therefore, how to adopt low alloyed component design and simple and effective process route to prepare a new generation of ultra-high strength steel material with excellent elongation rate is a significant work.
In recent years, bainitic steels with ultra-high strength are receiving attention from the iron and steel community. As retrieved:
the professor Bhadeshia of university of Cambridge, england, et al, uses the inhibition of Si on carbide precipitation to prepare carbide-free bainitic steel, the microstructure of which is nano or sub-nano superfine bainite, residual austenite and a small amount of martensite, and the strength can reach 2500MPa. The bainite steel meets the development targets of the new generation of ultra-high strength steel, can be used in the fields of bridge construction, machinery manufacture, vehicle engineering, marine ships and the like, can also be used in the special fields of heavy-duty train bogies, large-scale conveyor landing gear and the like, has wide application prospect, and becomes the new generation of ultra-high strength bainite steel for key research and development. However, the method has the problems of adding a large amount of noble alloy elements, long bainite low-temperature transformation period, difficult matching of high strength and high elongation, and the like.
The document with the Chinese patent publication number of CN 102071362 discloses a high-performance low-carbon bainitic steel and a production method thereof, and the production process comprises the following steps: the top and bottom composite smelting of the converter is required to be subjected to LF refining treatment, microalloying and Ca treatment, continuous casting and two-stage controlled rolling. The method belongs to Mn-Cr-Mo-Nb-Ti alloy systems, has the problems of complex total addition of alloy elements, complex production process and the like, and the strength of the produced bainitic steel is only 690Mpa.
The document of Chinese patent publication No. CN 102112648 discloses a "bainitic steel and a manufacturing method thereof", wherein the prepared bainitic steel has better comprehensive performance, but the heat treatment process is complex, various noble alloy elements are added, the minimum phase change time is as long as 8 hours, and the bainitic steel is not suitable for industrial production.
In order to improve toughness of steel, structures such as ferrite, bainite, martensite, and retained austenite are formed in steel, and the strength is not sufficient, but is generally lower than 800Mpa, as in the documents of chinese patent publications CN 101705431, CN 102251173, CN 1521285, and CN 101230444.
In summary, the problem that the high strength and the high elongation are difficult to be achieved simultaneously exists in the preparation process of the ultra-high strength bainitic steel. Research shows that the residual austenite has important influence on the hardness, impact toughness and wear resistance of steel materials, and the residual austenite is a non-stable toughness phase, and compared with martensite, the residual austenite has low hardness, easy deformation, high plasticity and toughness. Many factors influence the stability of retained austenite, including carbon content, grain size, morphology, and the like. Research shows that when the carbon content in the residual austenite is very low, the residual austenite has poor stability, is easy to be transformed into martensite in the strain process, and is not beneficial to improving the elongation; when the carbon content in the residual austenite is high, the residual austenite is too stable, is difficult to be transformed into martensite in the strain process, and is not beneficial to improving the elongation. When the retained austenite grain size is large, the retained austenite is unstable, and the influence on the elongation of the material is small. Studies have also shown that the thin film-like retained austenite is more stable than the bulk retained austenite, and contributes more to the elongation of the material. Therefore, the matching degree of the ultra-high strength and the high elongation is directly determined by optimally controlling the factors such as the carbon content, the size, the morphology and the like of the residual austenite in the ultra-high strength bainitic steel.
At present, research on the stability of retained austenite at home and abroad is generally focused on the aspects of heat treatment technology, chemical components and the like. In the preparation process of the ultra-high strength bainitic steel, precious alloy elements are usually added for improving the strength and the elongation, or a heat treatment process is improved, so that the cost is high, the production period is long, and certain energy waste is caused. The elongation of the produced ultra-high strength bainitic steel is generally lower and is generally lower than 10 percent.
In the literature published in journal of metallogy (2021,57 (6): 749-756) & lt deformation on ultra-high strength bainitic steel structure and mechanical properties, high strength bainitic steel with good plasticity, namely tensile strength and elongation of 1733MPa and 15.7% respectively, is prepared by adopting a deformation+bainitic isothermal treatment mode, but segregation is easily caused due to the fact that the Mn content is as high as 2.8wt.%, the deformation temperature is too low (only 300 ℃), the problem of plate surface quality is easily caused, the load of a rolling mill is increased, the energy consumption is increased, and moreover, the isothermal time at 300 ℃ is as long as one hour, and the production period is prolonged.
Disclosure of Invention
The invention aims to overcome the defects existing in the prior art and provide the high-strength high-plasticity bainitic steel with the yield strength of 1392-1435 MPa, the tensile strength of 1771-1900 MPa, the elongation of 16.6-19.2%, the strength-plastic product of 31.0-34.58%, good surface quality, low energy consumption of the deformation process and short production period and the production method.
Measures for achieving the above object:
a high-strength high-plasticity bainitic steel comprises the following chemical components in percentage by weight: c:0.35 to 0.65 percent, si:1.72 to 2.12 percent of Mn:2.30 to 2.55 percent of Al: 0.30 to 0.57 percent, and the balance of Fe and unavoidable impurities; metallographic structure: the volume ratio of bainite is not less than 67%, the volume ratio of retained austenite is 18-25%, and the volume ratio of martensite is not more than 15%.
Preferably: the weight percentage content of the C is 0.54-0.65%.
Preferably: the weight percentage content of Si is 1.72-1.92%.
A method for producing high-strength high-plasticity bainitic steel, which comprises the following steps:
1) Austenitizing the plate with the thickness of 8-10 mm after hot rolling, heating to 1105-1198 ℃ at the heating speed of 3-5 ℃/s, and preserving the temperature for 15-20 min;
2) Performing primary cooling, and cooling to 902-931 ℃ at a cooling speed of 5-10 ℃/s;
3) Performing first pass high temperature rolling pre-deformation with deformation rate of 0.1-1 s -1 The rolling reduction is 50-70%;
4) Cooling for the second time, and cooling to 10-30 ℃ above the start transition temperature Bs of the bainite at the cooling speed of 5-10 ℃/s;
5) Performing secondary rolling deformation, wherein the deformation adopts two-pass rolling, and the deformation rate of each pass is 0.1-1 s -1 The deformation rate of the two passes is 20-30% and the deformation rate of each pass is the same;
6) Cooling for the third time, cooling to 50-100 ℃ below the bainite starting transition temperature Bs at the cooling speed of 5-10 ℃/s, and preserving heat for 30-50 min at the temperature;
7) Air-cooling to room temperature.
The method comprises the following steps: the bainite starting transition temperature Bs point is 415 to 501 ℃.
The action and mechanism of each raw material and main process in the invention:
c: carbon is an austenite stabilizing element and can play a role in solid solution strengthening. Too low a carbon content is detrimental to the formation of retained austenite; the high carbon content reduces the weldability and toughness of the plate. Thus, the carbon content is controlled to be in the range of 0.35 to 0.65%, preferably the weight percentage content of C is 0.54 to 0.65%.
Si: cementite is easy to form in bainitic steel, plasticity is reduced, the cementite formation can be inhibited by adding 1.72-2.12% of silicon, the silicon content is too low, the inhibition effect is poor, red iron scale is easy to form due to the too high silicon content, the surface quality problem is caused, and the weight percentage of Si is preferably 1.72-1.92%.
Mn: manganese is an important strengthening element in steel, has a large influence on bainite transformation, and can increase the hardenability of the steel. The manganese content is too low, high-temperature phase transformation is easy to occur, a bainite structure cannot be obtained, the strength can be improved by increasing the Mn content, austenite is stabilized, and when the Mn content is too high, serious segregation is easy to occur, so that the performance fluctuation is large. Therefore, the manganese content is controlled to be in the range of 2.30 to 2.55%.
Al: for bainitic steel, the bainitic transformation rate is reduced along with the increase of the carbon content, and in order to shorten the production period, a proper amount of aluminum is added, so that the bainitic transformation can be accelerated, but the aluminum content is too high, and the quality of a casting blank is easily reduced. Therefore, the aluminum content is controlled to be in the range of 0.30 to 0.57%.
One of the key points of the invention is that the low temperature (10-30 ℃ above the temperature of Bs) is adopted for small deformation, if the temperature exceeds the temperature of Bs by more than 30 ℃, the deformation can prevent bainite transformation, and the bainite transformation quantity is reduced. The control of the deformation amount has strict requirements, the transformation range of the bainite is most easy to accelerate within 20-30%, more residual austenite can be obtained at room temperature, and the transformation of the bainite is blocked when the deformation exceeds 30%. After deformation, cooling to 50-100 ℃ below the temperature of the Bs point, so that fine bainite laths are more easily obtained, and when the temperature exceeds 100 ℃ below the temperature of the Bs point, the temperature is too low, and the bainite transformation time is long. In addition, the deformation temperature of the invention is above 425 ℃, thereby avoiding the problem of the surface quality of the plate, reducing the load of a rolling mill, reducing the energy consumption, and shortening the production period because the bainite phase change time is not more than 50 min.
The microstructure of the ultra-high strength bainitic steel prepared by the method is nano-scale (100-300 nm) lath bainite and film-shaped residual austenite (volume percentage is 25-40%). Firstly, adopting high-temperature (902-931 ℃) pre-deformation to reduce the size of austenite grains and promote fine grain strengthening, and then adopting low-temperature (10-30 ℃ above the Bs temperature) small deformation to accelerate isothermal bainite phase transformation; secondly, the bainite transformation quantity can be increased by small deformation at low temperature, and compared with non-deformed austenite, the bainite transformation quantity in the deformed austenite is increased by 30-50%, the size of the bainite lath is finer, and the strength is further improved; finally, the dislocation density of the matrix is increased due to deformation, the stability of the parent phase austenite is fixedly enhanced, more residual austenite is obtained at room temperature, and an excellent plasticizing effect is exerted, so that the plasticity of the material is improved. In summary, for high-strength bainitic steel, the plasticizing method of the invention can not only improve the strength of bainitic steel, but also increase the elongation, and obtain good matching of ultra-high strength and high elongation.
Compared with the prior art, the alloy element is the most basic element, namely Fe, C, si, mn and a small amount of Al, and the cost is low; the method of austenite pre-deformation and isothermal bainite phase transformation is adopted, the production process is simple, the preparation period is short, no additional equipment is needed, and the preparation process is environment-friendly; the prepared ultra-high strength bainite steel has excellent plasticity: yield strength is 1392-1435 MPa, tensile strength is 1771-1900 MPa, elongation is 16.6-19.2%, and strength-plastic product is 31.0-34.58%; according to the invention, the structure is thinned through austenite pre-deformation, the bainite transformation is accelerated, the stability of the retained austenite is improved, the excellent plasticity of the retained austenite is exerted, and the comprehensive mechanical properties of the bainitic steel are effectively improved.
Drawings
FIG. 1 is a diagram showing a metallographic structure of the steel of the present invention.
Detailed Description
The present invention will be described in detail below:
table 1 is a listing of chemical components of each example and comparative example of the present invention;
table 2 is a list of the main process parameters for each example and comparative example of the present invention;
table 3 shows a list of performance test cases for various embodiments of the present invention.
The embodiments of the invention are produced according to the following steps:
1) Austenitizing the plate with the thickness of 8-10 mm after hot rolling, heating to 1105-1198 ℃ at the heating speed of 3-5 ℃/s, and preserving the temperature for 15-20 min;
2) Performing primary cooling, and cooling to 902-931 ℃ at a cooling speed of 5-10 ℃/s;
3) Performing first pass high temperature rolling pre-deformation with deformation speedThe rate is 0.1 to 1s -1 The rolling reduction is 50-70%;
4) Cooling for the second time, and cooling to 10-30 ℃ above the start transition temperature Bs of the bainite at the cooling speed of 5-10 ℃/s;
5) Performing secondary rolling deformation, wherein the deformation adopts two-pass rolling, and the deformation rate of each pass is 0.1-1 s -1 The deformation rate of the two passes is 20-30% and the deformation rate of each pass is the same;
6) Cooling for the third time, cooling to 50-100 ℃ below the bainite starting transition temperature Bs at the cooling speed of 5-10 ℃/s, and preserving heat for 30-50 min at the temperature;
7) Air-cooling to room temperature.
Table 1 list of chemical components (wt.%) of each example and comparative example of the present invention
TABLE 2 list of the main process parameters for each example and comparative example of the present invention
Continuous table 2
TABLE 3 mechanical property test results list for each example and comparative example of the present invention
It can be seen from table 3 that the strength and plasticity of the ultra-high strength bainitic steel prepared by the method are further improved: the yield strength is 1392-1435 MPa, the tensile strength is 1771-1900 MPa, the elongation is 16.6-19.2%, and the product of strength and plastic is 31.0-34.58%. While the yield strength of the comparative example is 899-1203 MPa, the tensile strength is 1200-1898 MPa, the elongation is 7.5-16%, and the product of strength and plastic is 14.2-19.2%. The invention adopts low alloyed component design and simple and effective process route to prepare the ultra-high strength steel material with high strength and high elongation rate, has the characteristics of low cost and simple process, can be widely applied to the fields of mechanical manufacture, vehicle engineering, construction, shipbuilding and the like, and has higher practical application value.
This embodiment is merely a best example and is not intended to limit the implementation of the technical solution of the present invention.
Claims (5)
1. A high-strength high-plasticity bainitic steel comprises the following chemical components in percentage by weight: c:0.35 to 0.65 percent, si:1.72 to 2.12 percent of Mn:2.30 to 2.55 percent of Al: 0.30 to 0.57 percent, and the balance of Fe and unavoidable impurities; metallographic structure: the volume ratio of bainite is not less than 67%, the volume ratio of residual austenite is 18-25%, and the volume ratio of martensite is not more than 15%;
the production method comprises the following steps:
1) Austenitizing the plate with the thickness of 8-10 mm after hot rolling, heating to 1105-1198 ℃ at the heating speed of 3-5 ℃/s, and preserving the temperature for 15-20 min;
2) Performing primary cooling, and cooling to 902-931 ℃ at a cooling speed of 5-10 ℃/s;
3) Performing first pass high temperature rolling pre-deformation with deformation rate of 0.1-1 s -1 The rolling reduction is 50-70%;
4) Cooling for the second time, and cooling to 10-30 ℃ above the start transition temperature Bs of the bainite at the cooling speed of 5-10 ℃/s;
5) Performing secondary rolling deformation, wherein the deformation adopts two-pass rolling, and the deformation rate of each pass is 0.1-1 s -1 The deformation rate of the two passes is as follows20-30%, and the deformation rate of each pass is the same;
6) Cooling for the third time, cooling to 50-100 ℃ below the bainite starting transition temperature Bs at the cooling speed of 5-10 ℃/s, and preserving heat for 30-50 min at the temperature;
7) Air-cooling to room temperature.
2. A high strength, high plasticity bainitic steel according to claim 1, wherein: the weight percentage content of the C is 0.54-0.65%.
3. A high strength, high plasticity bainitic steel according to claim 1, wherein: the weight percentage content of Si is 1.72-1.92%.
4. A method of producing a high strength, high plasticity bainitic steel as claimed in claim 1, comprising the steps of:
1) Austenitizing the plate with the thickness of 8-10 mm after hot rolling, heating to 1105-1198 ℃ at the heating speed of 3-5 ℃/s, and preserving the temperature for 15-20 min;
2) Performing primary cooling, and cooling to 902-931 ℃ at a cooling speed of 5-10 ℃/s;
3) Performing first pass high temperature rolling pre-deformation with deformation rate of 0.1-1 s -1 The rolling reduction is 50-70%;
4) Cooling for the second time, and cooling to 10-30 ℃ above the start transition temperature Bs of the bainite at the cooling speed of 5-10 ℃/s;
5) Performing secondary rolling deformation, wherein the deformation adopts two-pass rolling, and the deformation rate of each pass is 0.1-1 s -1 The deformation rate of the two passes is 20-30% and the deformation rate of each pass is the same;
6) Cooling for the third time, cooling to 50-100 ℃ below the bainite starting transition temperature Bs at the cooling speed of 5-10 ℃/s, and preserving heat for 30-50 min at the temperature;
7) Air-cooling to room temperature.
5. A method of producing a high strength, high plasticity bainitic steel according to claim 4, wherein: the bainite starting transformation temperature Bs is 415 to 501 ℃.
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| CN115725900A (en) | 2023-03-03 |
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Inventor after: Hu Haijiang Inventor after: Wang Lifan Inventor after: Gan Xiaolong Inventor after: Zhou Mingxing Inventor after: Tian Junyu Inventor after: Chen Guanghui Inventor after: Liu Man Inventor after: Xu Guang Inventor before: Hu Haijiang Inventor before: Wang Lifan Inventor before: Gan Xiaolong Inventor before: Zhou Mingxing Inventor before: Tian Junyu Inventor before: Chen Guanghui Inventor before: Liu Man Inventor before: Xu Guang |