Patent Application
20210285069
The present application relates to alloy steel and ferrous metallurgical products for offshore engineering, in particular a grade R6 steel and chain for offshore mooring in the steel series for offshore mooring chain and the evaluation of its offshore environmental performance degradation resistance.
A mooring system is acquired for positioning and mooring with floating bodies in the process of the marine exploration, deep-sea oil and gas extinction, national defense construction and so on. The main component of the mooring system is offshore mooring chain by the steel. According to the standard in DNVGL (Det Norske Veritas-Gemtanischer Lloyd) named Offshore Standards, DNVGL-OS-E302 Offshore mooring chain. Edition July 2018, the offshore mooring chain can be classified into six grades called R3, R3S, R4, R4S, R5, and R6 according to its strength grading. The tensile strength of the chains at all grades after overall quenching-tempering shall be equal or greater than 690 MPa, 770 MPa, 860 MPa, 960 MPa, 1000 MPa, and 1100 MPa respectively. The grade R5 is the highest grade of the mooring chain produced and used at home and abroad by the first half of the year of 2018.
The long mooring chain for positioning can be divided into two types which are stud and studless for drilling type and production type of the floating bodies respectively. The length of a single chain can reach several kilometers. Alloy steel bars of diameter 52-230 min are used accordingly. All offshore mooring chain steels have an ultrahigh strength, as marine steel with a tensile strength above 690 MPa is ultrahigh-strength steel according to DNVGL.
The qualified mechanical properties and service performance of the offshore mooring chain are requisite in the offshore environment. When the strength of the chain is obtained by heat treatment of the final product, its toughness, especially the toughness of the flash weld area, must be ensured for the safety and reliability for resisting wild winds and huge waves. The chain is usually continuously treated in a special vertical furnace, i.e. the final performance of the chain is obtained after continuous quenching and tempering heat treatment. The accessories are forged from the steel, and their final properties are obtained through intermittent heat treatment.
It is seen that more than 5 h % of accidents have something to do with offshore mooring chains from the statistics of frequent accidents of floating bodies in the past decades. There have even been catastrophic accidents in which the platform capsized caused by the fracture of the chain.
From 2008 to 2018. Slow Strain Rate Testing (SSRT) in seawater was used to evaluate the degradation resistance of offshore environmental performance of the grade of the offshore mooring chain whose tensile strength ≥960 MPa and has high strength and toughness, so as to realize the lightweight of offshore floating bodies through ultrahigh-strength and ensure its service reliability at the same time.
DNVGL has defined grade R6 chain as the extreme technology and performance of the offshore mooring chain since 2013, and the provisional standard was not be terminated until 2018. DNVGL officially announced a standards including the grade R6 chain, specifying the performance of the chain and the basic process requirements of the production of the chain steel in July 2018.
DNVGL also proposed an additional standard named Class programme-DNVGL-CP-0237, Edition July 2018, Offshore mooring chain and accessories which evaluates the EAC (environment assisted cracking) of grade R6 chain under CP (cathodic protection) conditions according to the standards of ASTM G129 and ASTM E1820. The specific requirement is to carry out two tests: the one is SSRT with the applied potential of −850 mV, −1200 mV (saturated calomel electrode SCE) and strain rate of ≤10−5/s, the other is the KIEAC test (fracture toughness type 1 in seawater) with CT (compact tension) specimen, applied potential of −950 mV, −1050 mV (SCE) and the test speed of ≤6×10−9 m/s in seawater. So as to evaluate the degradation resistance of grade R6 chain in the seawater environment.
The seawater environment is generally considered as the service forbidden zone for ultrahigh-strength steel with yield strength over 1000 MPa.
As mentioned before, the main way to lighten the chain is ultrahigh intensification. There is a restraining relationship each other between strength and toughness, and the same is true of the relationship between strength and deterioration resistance of service performance in the seawater environment. Once the strength is improved, there must be a decrease of toughness, plasticity and the degradation resistance in the seawater environment performance. But according to DNVGL, when the strength is increased, the toughness is increased instead of decreasing with its EAC evaluated at the same time.
Although there is the kind of steel meeting the mechanical properties requirements of the grade R6 chain produced by the existing technology, DNVGL proposes the above additional requirements for the evaluation of EAC of the chain by impressed cathodic protection potential of the grade R6 chain for the sake of reliability. This is a new challenge in the research and development of the ultrahigh-strength chain.
There is a China Invention Patent No. CN103667953B named An Ultra High Strength and Toughness Offshore Mooring Chain Steel with Low Environment Assisted Cracking Sensitivity and its Manufacturing Method, which discloses the composition range of the grade R6 chain steel and its mechanical properties with quenched-tempered, and provides the service performance constant of the steel in the seawater environment, that is, corresponds to the critical hydrogen content of the determining fracture strength without hydrogen embrittlement crack and the threshold value of fracture toughness without stress corrosion crack in seawater as quenched-tempered. The invention has passed the acceptance of the expert committee organized by the Ministry of industry and information technology, as actural product, the steel and the chain in the invention meet and exceed the temporary standards of mechanical properties and seawater environmental service performance of the grade R6 chain, Vanadium are the element for refining or strengthening effect in the form of VC in the invention. The invention does not cover the technology to balance corrosion potential and cathodic protection potential to prevent embrittlement by hydrogen generation of the chain caused by cathodic overprotection, coping with new standard.
The content of evaluating the embrittlement by hydrogen generation caused by cathodic protection is added in the latest standards of DNVGL2018 under the premise of ensuring the mechanical properties of the chain. While the reliability of the chain mainly depends on the overall performance given by the steel.
There is another Chinese invention patent No. CN101161843A named A Method to Improve the Utilization Ratio of Vanadium Alloy with V-N (vanadium-nitrogen) Micro-alloyed High Strength Steel, which proposed the process to control the V/N ratio of air-cooled steel to the range of 4≤V/N≤6 and the precipitation of VN. Because Al (aluminum) is the deoxidizer of low-carbon deoxidized killed steel, and there is an unavoidable residual Ti (titanium) with more affinity with N (nitrogen). When the proportion of the residual Al in the molten steel from the embodiment of the invention is 0.025-0.035 wt %, and the majority of N has been consumed by TiN (titanium nitride) and AlN (aluminum nitride) formed in the early stage, it is impossible to come into being VN, and it is impossible to realize the expectation of 4≤V/N≤6 too.
The utilization of nitrogen as austenitic grain refinement elements whose content is in the range of 0.006-0.024 for a class of offshore mooring chain steel and the precise matching technology of Ti, Al, Nb, and V are disclosed in A Heat Treatment Method for a Class of Offshore Mooring Chain Steels and its Chain, Invention Patent, China, No. CN201611001805.3.
And there is another China invention patent application No. 201810638000.2 titled A Kind of ultrahigh-strength and Toughness Steel with Tensile Strength of 1100 MPa and its Manufacturing Method. The invented steel is specified to be used to manufacture the grade R6 high-performance offshore mooring chain for offshore platforms and others. The C content of this invented steel is 0.245-0.350% and the steel has the microstructure of tempered martensite and tempered bainite and retained austenite. From the embodiments in this invention No. 201810638000.2 which will be one of the contrast embodiments in present invention, it can be seen that the surface after quenching is all martensitic microstructure with low transformation temperature and strong cooling crack sensitivity. The toughness of base and weld of the chain are reduced below the qualified line by coarse eutectic niobiumcarbide. The air cooling process is impossible to be implemented in the continuous heat treatment production line to avoid the tow-temperature phase transformation crack although this patent requires air cooling after heat treatment. In addition, retained austenite will decompose during the high-temperature tempering although austenite is beneficial to toughness and environmental performance.
Higher content of N has a greater driving force for precipitation, higher density of precipitation phase, and greater strengthening effect compared that with the low content of N in the steel contained V
The technical problem to be solved by the present invention is to propose a new manufacturing scheme of a grade R6 offshore mooring chain as well as its steel for use in anchoring and mooring floating bodies with cathodic protection.
The precipitation strengthening effect and the toughness and a low corrosion rate of the chain are improved on the premise of ensuring the hardenability and reduces the corrosion potential when the total contents of alloy and microalloy are narrowed, to curb the embrittlement by hydrogen generation due to the chains are received by cathodic overprotection passively.
The specific scheme adopted by the present invention is as follows.
I. The Chemical Composition of the Steel for Grade R6 Offshore Mooring Chain with High Strength and High Toughness
The chemical composition by wt % (percentage by weight) are as follows: C 0.18˜0.24%, N 0.006˜0.024, P 0.005˜0.025, S≤0.005, Si 0.15˜0.35, Mn 0.20˜0.40, Cr 1.40˜2.60, Ni 0.80˜3.20, Mo 0.35˜0.75, Cu≤0.50, Al≤0.02, Ti≤0.005, V 0.04˜0.12, Nb 0.02˜0.05, Ca 0.0005˜0.004, O≤0.0015, H≤0.00015, the rest is Fe and unavoidable impurity elements.
It is further defined that 0.22<(C+N)<0.26; the total content of alloy ΣM=(Si+Mn+Cr+Ni+Mo+Cu), and 3.4<ΣM≤6.8: the total content of microalloy ΣMM=(Ti+Al+Nb+V), and 0.065<ΣMM≤0.194.
The content of N in the chemical composition is 0.016-0.024.
The chain is made of round bars corresponding to the above chain steel.
The present invention further limits the content of C and N and the range of ΣM and ΣMM on the basis of the related product composition applied by two the Chinese invention patents whose publication numbers are CN103667953 B and CN106636928A.
(1.1) The total content of narrowed alloy elements is ΣM=(Si+Mn+Cr+Ni+Mo+Cu).
(1.2) The total content of narrowed microalloy elements is ΣMM=(Ti+Al+Nb+V).
(1.3) The content of N is increased by a large margin and the content of C+N is controlled to make up for the decrease of strength and toughness caused by the narrowed range of additive alloy content, and the compensation theory can be seen below.
(1.4) In prior arts, the formation of TiN by using Ti in low-alloy steel is to prevent austenite grain glowing. Although the solid solubility product of Ti and N is very small, the ability to refine grains is constrained due to the large scale of TiN precipitated at high temperatures. In the present invention the content of residual Ti in the steel is controlled for two reasons: one is to reduce the consumption of N caused by Ti, ensure the N content of NbCN, and reduce its solid solubility product so as to improve its ability of hindering the growth of austenite grain, and improve the N content of VCN; the other is to prevent Ti from polluting the steel ladle.
(1.5) The main deoxidizing element of the steel in the present invention is Al, which is used for sufficient peroxidation. And the content of residual Al after the final deoxidation is controlled no more than 0.02 to reduce the consumption of N caused by Al.
(1.6) The Nb content in the present invention is limited to 0.02-0.05, and NbCN is precipitated from the steel, and the effect of NbCN inhibiting the growth of austenite grain is stronger than that of NbC. After the steel is made into the chain link, the chain temperature is increased from ≤920° C. to ≥980° C. during the quenching heating, and microstructure of the chain after austenitizing is transformed into BU (upper bainite) during cooling. The initial phase transformation temperature of BU and martensite is Bs and Ms, respectively, and Bs(˜500° C.) is higher then Ms(˜320° C.). The cooling crack sensitivity decreases with the increase of the phase transformation temperature.
(1.7) The V content in the present invention is controlled to be from 0.04 to 0.12, and when the content of the residual N is ensured, there is VCN precipitates with an average size of 2 nm in the chain during tempering and nearly half of the total amount of V corresponds to a chemical equivalent ratio of V:N=3.6 in the VCN precipitated, which are used to improve the strength and toughness of the steel.
II. Based on the Chemical Composition of the Present Application, the Precipitation of the Offshore Mooring Chain Steel of the Present Application Follows the Rules Below.
(2.1) The nitride and carbonitride are controlled to be precipitated in the sequence of TiN—AlN—NbCN—VCN, on the basis of the general technology that is smelting, bloom continuous casting, blooming with high-temperature heating, intermediate billet heating, forging or rolling, chain making, flash welding and heat treatment and so on. The solubility product of [Nb] [C+N] is smaller, and the effect of inhibiting the growth of austenite grain of [Nb] [C+N] is stronger than that of NbC. The existence of NbCN allows the temperature of the chain to increase from ≤920° C. to ≥980° C. before quenching. In addition, there is to the drag effect of solid solution of Nb on the grain boundary.
(2.2) The existing technology shows that the strengthening effect of VCN is better than that of VC, especially for the very fine MCN carbide with an average size of 2 nm precipitated by tempering. In the present invention, the quenching temperature is increased, therefore M3C, M2C and VCN is fully solid soluble. In the present patent, V is as MCN (where M=V, Mo) to precipitate and increase the strengthening effect during tempering instead of being an element to prevent the growth of austenite grain in existing technologies. As the main composition of M in MCN is V, MCN is also expressed as VCN in engineering.
(2.3) Al is used as the main deoxidizing element and the subordinate element to increase the austenite coarsening temperature. By limiting the residual acid-soluble Al, i.e. Als, the consumption of N by Al can be reduced, and the residual content of N combined with Nb and V can be increased, that is to say, NbCN and VCN can be formed with the former effectively improving the austenite coarsening temperature and the latter increasing the strengthening effect.
(2.4) According to the equivalent ratio, Ti:N=3.4. Al:N=2:1, Nb:N=6.6. V:N=3.6. As compared with AlN. NbN has a stronger effect of preventing the growth of austenite grain and the N consumption of Nb is nearly 30% that of Al when the content the same as Al. Based on this, this application promotes the final combination of N with Nb and V through accurate control of element content.
(2.5) Even if Ti is not added in the steelmaking process of low or medium alloy structural steel, the final precipitation is usually VC rather than VN (VCN), as there is a large consumption of N caused by Ti brought in by raw materials and refractories, and caused by the residual Al before tapping as specified in the standard. Up to now, various technologies for controlling V/N ratio are difficult to implement accurately, and the present invention solves this problem by controlling the V content and increasing the N content in VC on the basis of the technology of controlling Ti. Al and Nb by adding N. See Table 1 for the examples of estimates of precipitates, nearly half of the total amount of V corresponds to a chemical equivalent ratio of V:N=3.6 in the VCN precipitated by tempering.
III. The Characteristics of Microstructure in the Offshore Mooring Chain Based on the Chemical Composition and Precipitation Rules of the Present Application
Due to the combination and limited amount of alloy elements, the chain link is transformed into a composite bainite microstructure consisting of BU (upper bainite) with a small amount of BL (lower bainite) and M (martensite) during the cooling process after austenitizing. Take the position that has a distance that is about a third of radius from the surface of the chain for example, the volume fraction of BL+M is no more than 10%, without granular bainite and ferrite. The bainite microstructure with a higher phase transformation temperature is favorable for the full quenching of the whole section of the large diameter chain with poor cooling conditions and solves the problems of the large difference of microstructure and properties between the surface and the internal of the large diameter chain and the sensitivity of cooling cracks.
The phase transformation temperature of BU with Bs˜500° C. is higher than that of the martensite with Ms of ˜320° C. The cooling crack sensitivity decreases with the increase of the phase transformation temperature.
IV. Based on the Chemical Composition, Carbide Precipitating and Optical Microstructure. Laboratory Corrosion Potential and EAC of the Finished Product Chain of the Application
According to the requirements of users to evaluate EAC in advance, making chain and simulated quenching-tempering of the chain link are carried out first, then EAC test is carried out by sampling.
(4.1) Corrosion potential: the flat specimen from the chain is sampled and immersed in the artificial seawater prepared in accordance with ASTM d1141, and after immersion at the room temperature of 25° C. for 80 hours, the laboratory stable corrosion potential is measured to be about −610 to −650 MV (SCE, reference calomel electrode);
(4.2) EAC of the chain is evaluated in accordance with the standard of DNVGL-CP-0237.
(4.2.1) SSRT: SSRT is carried out in the atmosphere and in artificial seawater, with no potential or with potential of −850 mV, −1200 mV (SCE); SSRT with axial cylindrical smooth specimen whose strain rate is ≤10-5/s; Z0 and ZE are the reductions of area measured with no potential and with potential after specimens are broken respectively; the Z0/ZE ratio indicates the degradation degree of EAC resistance.
(4.2.2) The KIEAC test of CT specimen: in artificial seawater, hydrogen is precharged for 48 hours when the potential is not applied, or applied by −950 mV and −1050 mV (SCE). Then, stretch with a speed of ≤6*10−9 m/s, when no potential is applied, or the potential of −950 mV and −1050 mV (SCE) is applied. KQEAC
When the KQEAC specimen meets the plane strain condition, the KIC data is obtained, and the EAC here is expressed as KIEAC
KQEAC of the weld zone of the chain is also tested for comparing the performance of the weld zone with that of the base.
The examples of implementation has been listed the results of EAC test, and the data of the present invention is favorable when −950 mV, −1050 mV potential is applied.
The chain of the present invention is made of round bar having the corresponding chemical composition, and the round bar is processed in sequence by chain making, flash butt welding, and heat treatment to obtain the final product wherein the heat treatment include high-temperature quenching with ≥980° C. and tempering with 600° C. to 690° C. Quenching and tempering are cooled with water less than 50° C.
Round bar is made from continuous casting bloom or ingot having corresponding chemical composition, and in sequence by heating, blooming, rolling and slow cooling, in which the heating temperature is more than 1230° C. so that nitride and carbonitride are all dissolved in austenite; in the cooling process, due to the combination of micro-alloying elements MM and the limit of C+N, the precipitation sequence of nitride and carbonitride is TiN—AlN—NbCN-MCN.
The nitride and carbonitride are controlled to be precipitated in the sequence of TiN—AlN—NbCN-MCN on the basis of the general technology, that is smelting-bloom continuous casting-blooming with high temperature heating-intermediate billet heating-forging or rolling-chain making-flash butt welding-heat treatment, and so on. The solubility product of [Nb][C+N] is smaller, the effect of inhibiting the growth of austenite grain of NbCN is stronger than that of NbC, and the existence of NbCN (and solid solution of Nb) allows the temperature of the chain to increase from ≤920° C. to ≥980° C. before quenching.
Compared with the available technology, the characteristics of the present invention focus on:
The size of the effective grain for toughening is smaller because of the existence of substructure;
The present invention is further described in detail with reference to carrying out example.
Carrying out example (invention example) 1-4 and contrast example 3 are about the process wherein continuous casting bloom with tire size of 390×510 mm are rolled into the round bars with a diameter of 120 mm, while contrast example 1, 2 and 4 are about the process that 420 kg test ingots are forged into round bars with a diameter of 95 mm, and then the round bars are processed in sequence by blanking, heating, bending, flash welding, forming chain and heat treatment (quenching+tempering) to obtain the finished chain. The performance data is the average value of the results of three groups of specimens. Numerical treatment of the third place after the decimal point: ≤discard and ≥6 into 1.
See Table 2 for the chemical composition of carrying out example 1 to 4 and contrast examples 1 to 4. See Table 3 for process parameters and performance of the chain, and see Table 4 for the size and test results of CT specimens. Some of the results of Table 4 have been collated and included in Table 3.
Loading test: Zwick 50 kN testing machine, made by Zwick Co., Germany; prefabricated fatigue crack: MTS 810 (100 kN) electro-hydraulic servo testing machine system, made by MTS. Co., America; corrosion test device: seawater corrosion test container, equipped with slow tension and compact tension fixture; potentiostat: CHI660D electrochemical workstation. Shanghai Chenhua Instrument Co., China; pH value of artificial seawater is 8.2-7.0; 25° C. See
The EAC test conditions are in accordance with DNVGL-CP-0237: EAC test is additionally requited for the grade R6 chain. The SSRT and KIEAC (CT) test is included to evaluate EAC resistance. The SSRT test is carried out with no potential, potential of −850 mV, −1200 mV (SCE) and axial cylindrical smooth specimen in dry atmosphere and artificial seawater. The CT test is carried out with potential of −950, −1050 mV (SCE) and in artificial seawater. ZE/Z0 and KQEAC
The results show that there is no significant difference between SSRT data of steel in a dry atmosphere and those in an artificial seawater environment, and all of them fluctuate within the error range. SSRT of the atmospheric environment is omitted in both The carrying out example and the contrast examples.
Z0 and ZE refer to the results of the reduction of area of SSRT without and with potential respectively. In artificial seawater, the potential is not added or added to −950 mV and −1200 mV (SCE). Strain rate ≤10−5/s.
KQEAC
KQEAC
According to users' requirement of forward lead EAC evaluation (Do it in advance at the steel mill), chain making and simulated quenching-tempering are carried out first, then EAC test is carried out by sampling. KQEAC of the weld zone of the chain is also tested for the comparison of the performance of the weld zone and the base.
Carrying out example (invention example) 1-4 all conform to the range of the composition limitation of the present invention. On the premise of controlling the minimum content of Ti (controlling is inevitable in the industrial scale), the limited TiN and AlN combined with a small content of N are first precipitated in the cooling process of continuous casting bloom, according to the solubility product from small to large, which ensures the subsequent precipitation of NbCN and VCN. When the heat temperature is more than 1230° C. the continuous casting bloom is forged and rolled. AlN, NbCN, VCN, M3C and M2C was first all dissolved in austenite, and then precipitated during cooling. Among them, TiN, NbCN, and AlN do not dissolve when the chain is quenched at 980° C. which hinders the growth of austenite grain. NbCN, which is still insoluble at 1150° C. is used as the main precipitate to hinder the growth of austenite grain. M3C, M2C, and VCN are fully solid solution with a high-temperature quenching at 980° C., and then precipitated again during a high-temperature tempering. The quenching-tempering steel is strengthened by fine and dense VCN, so as to make up for the loss of strengthening effect caused by reducing the total content of alloy in the present invention. There are excellent mechanical properties such as strength, plasticity and toughness and others, and it is outstanding that the low-temperature impact value of the base and the weld are higher than the standard requirements. And mechanical properties value is abundant. The processing properties are well too, which can be seen from that Bs is about 500° C. which is about 180° C. higher than contrast example's Ms 320° C., the phase transformation temperature is higher, and the crack sensitivity is lower.
In the carrying out example 1.2 and 4, the SSRT specimen was slowly stretched with applied potential −850 mV (SCE) in artificial seawater at a strain rate of ≤10−5/s, compared with the specimen without potential, the result shows that ZE/Z0=1, that is, the plasticity did not decrease. The contrast example 1, ZE/Z0=0.85. But when −1200 mV (SCE) is applied, the slow tensile specimen is seriously embrittled as ZE/Z0≤0.18 in both the earning out example 1, 2, 4 and the contrast example 1.
In the carrying out example 2, with −1050 mV (SCE) applied. KIEAC
In the carrying out example 3, with −950 mv (SCE) applied, the value of KQEAC
In the contrast example 3, with −1050 mV (SCE) applied. KQEAC
As a reference, the potential measured after immersion in seawater for 80 hours is used as the corrosion potential under laboratory conditions. The difference between corrosion potential and applied potential is overprotection potential.
Among them, the overprotection potential to −850 mV(SCE) in In the carrying out example 1 and 3 is about 200 and 232 mV (SCE) respectively, which are within the allowable range. However, the overprotection potential to −1200 mV (SCE) is about 550 and 580 mv (SCE) respectively, which is hard to bear.
The carrying out example 1, 2 is compared with the contrast example 4, the strength is increased by 62-75 MPa by adopting similar quenching-tempering treatment which shows that the strengthening effect of VCN is better than that of VC.
In the contrast example 1. Ms is low, it is sensitive to cooling crack, and C+N=0.293, which is exceeded the scope of the invention, and the impact value is unqualified. Coarse NbCN particles of 100 μm class were found. There are only VC precipitates, no VCN precipitates.
In the contrast example 2, Ms is low, and it is sensitive to cooling crack; N has a low content, N is exhausted by first precipitated NbCN, and is not enough to form AlN. The impact value is 61J, which barely conform with the standard, but the tensile strength is as low as 1080 MPa, which is unqualified. There are only VC, no VCN.
In the contrast example 0.3, the total content of alloy exceeds the scope of the invention. The difference between −850 mV and its corrosion potential of −520 mV, that is, the overprotection potential is about 0.330 mV (SCE). SSRT test show a tendency of embrittlement. The content of Nb is as high as 0.07, and NbCN is precipitated before AlN.
In the contrast example 4. Ms is low, it is sensitive to cooling crack; with the increase of Al and Ti, the total content of micro-alloy elements exceeds the scope of the invention. Due to the consumption of N, N was exhausted when NbCN was precipitated. There are only VC, no VCN. The yield ratio is 0.96 and greater than regulation 0.95. The strengthening and toughening effects are not obvious when the quenching temperature is at 980° C. Impact toughness is unqualified.
In a word, there is no VCN precipitation in the contrast examples 1.2 and 4, only VC is precipitated in tempering, and the precipitation strengthening effect of V is not ideal. And austenite grains are coarsened or begin to coarsen at 910° C. in all contrast examples: compared with all contrast example wherein there are fine austenite grains at the chain temperature of 980° C. and the tempering temperature is allowed to increase (up to 635° C. when in the contrast example 0.3), the performance and process parameters of the contrast examples are entirety lower than those of the carrying out example of the present application.
Besides the above carrying out example, the present invention further includes other carrying out examples, and any technical solution formed by equivalent transformation or equivalent substitution shall fall within the protection scope of claims of the present invention.
| Number | Date | Country | Kind |
|---|---|---|---|
| 201910306407.X | Apr 2019 | CN | national |
| Filing Document | Filing Date | Country | Kind |
|---|---|---|---|
| PCT/CN2019/087168 | 5/16/2019 | WO | 00 |
