CN101250607A - Grain refining method for ultra-supercritical steel - Google Patents
Grain refining method for ultra-supercritical steel Download PDFInfo
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Abstract
The invention relates to an ultra-supercritical steel grain refinement process which has high alloy content and obvious structural inheritance, which solves the problems of mixed crystal phenomenon of uneven grain, unstable ultra-supercritical steel property, and serious deterioration of ultra-supercritical steel material which are caused by the multiplex recycling reciprocation austenitization. The process comprises controlling the components of ultra-supercritical steel or partially trimming when in melting, wherein the mass fraction of Mn element is 0.8-1.2%, and the mass fraction of Nb is 0.06-0.08%, then refining grains through adopting the intermediate annealing technology after the even annealing of ultra-supercritical steel. The process combines the control and the trimming of steel components and the appropriate heat treatment technology, can significantly refine the ultra-supercritical steel grains which are used to produce generating equipment and has high alloy content through weakening structural inheritance effect, and obtains original finer austenite grain whose size <=10 mu m, thereby increasing the usage property of ultra-supercritical steel, especially increasing the impact ductility of ultra-supercritical steel significantly.
Description
Technical field:
The present invention relates to the alloy content height, have the supercritical steel crystal fining method of obvious tissue heredity, make the supercritical steel homogeneous microstructure, grain-size finally obtains good comprehensive mechanical properties below 10 μ m.
Background technology:
Along with the continuous deterioration of global ecological environment and exhausted day by day based on the Energy resources of fossil oil, can significantly improve thermo-efficiency, reduce exhaust gas emission, thereby realize that ultra supercritical firepower steam-electric power technology efficient, energy-saving and environmental protection receive much concern.Country's Eleventh Five-Year Plan clearly proposes, and one of emphasis of China's equipment manufacture is the development of million kilowatt ultra supercritical generating set from now on.So-called ultra supercritical generating set is meant working parameter---the pressure and the temperature of steam, is increased to 30～35MPa respectively, 593～600 ℃ or higher, and have the circulation system of double reheat.Yet the raising of steam parameter must be to being used to make the steel grade of ultra supercritical generating set---supercritical steel, with and complete processing stern challenge has been proposed.Therefore, the development of ultra supercritical unit, key is the research to ultra supercritical steel and its complete processing.
Up to the present, western developed country is being done the work that much has constructive meaning aspect the research and development of ultra supercritical steel, and has made the part steel grade realize commercialization, as contains the 10Cr type 9-12Cr steel of W.Yet, since comparatively complicated alloying constituent, the adding of more alloying element, and the austenite of supercritical steel is highly stable under supercooled state.Although very stable austenite can increase the hardening capacity of supercritical steel significantly, but when it takes place to ferritic transformation, always make the tissue (lath or slip) of the new ferritic phase that forms keep certain crystalline orientation relation with it, and cause in austenitization subsequently, taking place tissue heredity.Supercritical steel organize hereditary effect, make supercritical steel in the course of processing, the even crystal grain of tissue odds is thick, finally causes the supercritical steel over-all properties to worsen.
In order to solve the thick problem of the even crystal grain of tissue odds that the heredity of ultra supercritical structure of steel causes, existing technology normally adopts the austenitizing that repeatedly moves in circles, by repeatedly phase co-conversion between ferrite/austenite (γ α), ferrite/austenite in parent phase repeatedly repeatedly forming core come crystal grain thinning.Although the austenitizing that repeatedly moves in circles, can increase ferrite/austenite position of forming core again in parent phase, can play certain refining effect, because supercritical steel has stronger tissue heredity, prior art is limited to the degree of grain refinement of supercritical steel, if austenitizing temperature control is improper, also very easily produces the mixed crystal phenomenon of crystal grain inequality, cause the supercritical steel unstable properties, the material of serious deterioration supercritical steel.In addition, from the angle of manufacturing cycle and production cost, prior art---the austenitizing operation that repeatedly moves in circles is longer, the technological process more complicated, and technique controlling difficulty is bigger, causes manufacturing cost higher relatively.
Summary of the invention:
The crystal fining method that the purpose of this invention is to provide a kind of supercritical steel solves the mixed crystal phenomenon that the austenitizing that repeatedly moves in circles may produce the crystal grain inequality, causes the supercritical steel unstable properties, the problems such as material of serious deterioration supercritical steel.This method is in conjunction with steel grades control or part fine setting and appropriate thermal treatment process, organize hereditary effect by weakening, refinement is used to make the crystal grain that contains the high supercritical steel of alloy amount of generating set significantly, obtain the thin original austenite grain of size≤10 μ m, thereby can improve the use properties of supercritical steel, especially can improve the impelling strength of supercritical steel significantly.The present invention can obviously simplify supercritical steel heavy casting and forging generating set thermal treatment process in the actual production, reduce the actual production difficulty of supercritical steel heavy casting and forging generating set, and save the manufacturing cost of supercritical steel heavy casting and forging generating set.
Technical scheme of the present invention is:
A kind of crystal fining method of supercritical steel at first when smelting, carries out certain control or does the fine setting of part the composition of supercritical steel in it becomes sub specification, after supercritical steel is carried out homogenizing annealing, adopt intermediate annealing process then.Detailed step is as follows:
1. Composition Control or fine setting:, wherein Mn and Nb element are controlled and finely tuned according to the one-tenth sub specification of supercritical steel.The content of Mn element is increased to massfraction is about 0.8～1.2%; Meanwhile, guarantee that the content of Nb element is near the upper limit that becomes sub specification, massfraction about 0.06～0.08%.
2. the control of heat treatment process parameter: supercritical steel forms after the hot-work, and it is carried out homogenizing annealing.The homogenizing annealing temperature is controlled at approaching but is not more than the complete solvent temperature of fine precipitated phase MX, and scope is 1020～1100 ℃.Then, supercritical steel is carried out process annealing.The process annealing temperature is about Ac a little more than the Chernoff b point of the supercritical steel after Composition Control or the fine setting
3+ 60～150 ℃.
Physical metallurgy analysis of the present invention:
1) the present invention at first controls or finely tunes the composition of supercritical steel, promptly the content of Mn element is finely tuned to about 1%, the content of Nb element is controlled at the upper limit, about 0.06～0.08%, purpose has two: one, and by trickle increase Mn element, microstructure and the relation of the crystalline orientation between the original austenite tissue that supercritical steel is obtained are weakened.Mn element in the steel is an austenite former, has the austenite of expansion phase region, stablizes complete austenitizing temperature---the Ac of supercooled austenite and reduction steel
3The effect of point.Therefore, the increase slightly of Mn element, in ferritic phase (martensite or acicular ferrite) transforming process, can keep a certain amount of at supercooled austenite, do not change and be the remaining austenite (Fig. 1) of isolated little island as yet, this part remaining austenite continues to be transformed in continuous cooling process subsequently, its transmutation product and parent grain---and original supercooled austenite crystal grain does not have or has more weak crystalline orientation relation.And, isolated island shape remaining austenite tissue is dispersed in and original supercooled austenite crystal grain has on the ferritic phase matrix of certain crystalline orientation relation or between ferrite unit (slip or lath), it suppresses growing up and alligatoring of single ferrite unit (slip or lath) consumingly, thereby produces the structure refinement of supercritical steel.Moreover, little island structure is the residue supercooled austenite that changes as yet, it will inevitably the enrichment austenite former, these elements make these island structures become preferential nucleation site in austenitization subsequently, thereby significantly improve austenitic nucleation rate, finally realize the refinement of crystal grain.In addition, because the increase slightly of Mn element causes the complete austenitizing temperature Ac of supercritical steel
3Descend, this also causes the recrystallization temperature point of supercritical steel in austenitization---and Chernoff b point descends, thereby adopts lower annealing temperature can realize the recrystallization of ferrite to austenitic transformation, thus the crystal grain of refinement supercritical steel.The 2nd, by the content of control Nb element, make it reach into the upper limit of sub specification, so that generate the fine precipitated phase of MX type that contains the Nb element in a large number, disperse is distributed in the matrix, guarantee in follow-up heat treatment process, the new austenite grain boundary that forms moves largely and is suppressed by the fine precipitated phase of MX type behind the supercritical steel austenitizing, thereby hinders the growing up fast of supercritical steel austenite crystal, alligatoring, realizes the refinement of ultra supercritical structure of steel.
2) supercritical steel of process Composition Control or fine setting to its thermal treatment of annealing, comprises two kinds of thermal treatment process of homogenizing annealing and process annealing after finishing the shaping heat processing technique.The present invention realizes the supercritical steel grain refining by to two kinds of annealing heat treatment process parameters---the control of annealing temperature.The purpose of homogenizing annealing is some defectives that produce in uneven components or the hot procedure in order to eliminate, to reach composition and homogeneous microstructure.But, if the homogenizing annealing temperature is too high,,, in short man-hour, realize the homogenizing of composition as the rapid diffusion of W although can accelerate segregation element, this is easy to cause the serious alligatoring of crystal grain.And for the steel grade that contains just like V, Nb, these strong carbide forming elements of Ti, the homogenizing annealing temperature is too high, can make the precipitated phase dissolving that hinders crystal boundary migration, can suppress the fine disperse distribution of grain growth, growing up unusually of austenite crystal appears, cause mixed crystal phenomenon, this is histoclastic homogeneity seriously, thus the use properties of deterioration steel.Therefore, be about 1100 ℃ based on a large amount of solvent temperatures that contain the MX precipitated phase of Nb element in the supercritical steel through Composition Control or fine setting, the homogenizing annealing temperature of supercritical steel is controlled at and is not more than in 1100 ℃, to suppress crystal grain too alligatoring in the homogenizing annealing process of supercritical steel, and also in order to prevent to produce mixed crystal phenomenon, for supercritical steel realizes that in follow-up process annealing process grain refining and homogeneous microstructure have turned tissue into and prepared.Because the time of homogenizing annealing is generally all long, so after homogenizing annealing, often the grain-size of steel is comparatively thick.And for supercritical steel, improper if this just certainly will cause in the follow-up heat treatment process austenitizing temperature to be controlled owing to there is a tissue heredity, refine austenite crystal grain just will be difficult to realization.Because for parent grain---initial austenite crystal grain has the ferritic structure form of certain crystalline orientation relation, have two kinds of transformation situations in austenitization: a kind of situation is that the austenite crystal and the ferritic structure that form are kept certain crystalline orientation relation, finally in austenitization, grow up, be merged into ferritic structure parent phase---initial austenite crystal grain has the crystal grain of same orientation and same chip size, promptly organize hereditary effect; Another kind of situation is that the austenite crystal and the ferritic structure form that form do not have the crystalline orientation relation.In austenitization, although the new austenite crystal that forms has growing up to a certain degree, there is not tissue heredity in it, and usually by initial austenite crystal boundary place forming core and constantly grow to intracrystalline.The crystal boundary of the final new austenite crystal that forms is collided each other, reaches balance, thus obvious refinement initial austenite crystal grain, and this situation is austenitic recrystallization phenomenon.Generally speaking, in austenitization, both of these case exists simultaneously with competitive way.When austenitizing temperature is lower than a certain threshold value, organize heredity to occupy an leading position, and recrystallization can only occur in the crystal boundary place, observe a series of small grains of crystal boundary punishment cloth this moment easily, promptly so-called " grain boundary effect " at coarse grain; On the contrary, when austenitizing temperature is higher than a certain threshold value, recrystallization will be occupied an leading position, and initial austenite crystal will obtain tangible refinement.This threshold value is to be named as " Chernoff b point ".This shows, the temperature control of austenitizing, can direct relation realize the refinement of initial austenite crystal grain.For supercritical steel with obvious tissue heredity, want refinement homogenizing annealing coarse grain afterwards, must be by reaustenitizing, and the temperature of austenitizing is controlled at Chernoff b point " above a certain temperature, utilize austenitic recrystallization process to realize this purpose.So the temperature of process annealing should be controlled at Chernoff b point " above a certain temperature, for the supercritical steel through Composition Control or fine setting, this value is about Ac
3+ 60～150 ℃.
Beneficial effect of the present invention is:
Compared with prior art, the present invention reaches the effect of remarkable refinement ultra supercritical crystalline grain of steel, the grain-size that is obtained≤10 μ m by the control of simple Composition Control or fine setting and thermal treatment key process parameter.This and prior art---the thermal treatment process scheme of the austenitizing that repeatedly moves in circles is repeatedly compared, and when not only obviously shortening worker, reduces the production difficulty, and reduce power consumption of polymer processing and save product cost, and the even grain size that is obtained.Meanwhile, the refinement of crystal grain and the homogenizing of tissue make supercritical steel obtain very good comprehensive mechanical property, have higher intensity and good toughness.
Description of drawings:
The organization chart (500 *) of Fig. 1 Composition Control or fine setting back supercritical steel.
The ultra supercritical original austenite grain size (500 *) of Fig. 2 the invention process 1 gained.
The ultra supercritical original austenite grain size (500 *) of Fig. 3 the invention process 2 gained.
Embodiment:
The crystal fining method of supercritical steel of the present invention at first when smelting, is controlled or finely tuned the composition of supercritical steel, after supercritical steel carries out homogenizing annealing, adopts the intermediate annealing process crystal grain thinning then, and is specific as follows:
1. Composition Control or fine setting
When the ultra supercritical smelting steel carried out charge calculation, the Mn element was pressed massfraction 0.8～1.2% and is calculated, and the Nb element is pressed massfraction about 0.06～0.08% and calculated then to become the sub specification upper limit, and the tissue of Composition Control or fine setting back supercritical steel is seen Fig. 1.
2. thermal treatment process
1) after supercritical steel is finished the shaping heat processing technique, it is carried out homogenizing annealing, and the temperature of strict control homogenizing annealing.This temperature should be not more than a large amount of dissolved temperature of fine MX type precipitated phase that disperse is distributed, promptly 1020～1100 ℃.Heating rate, soaking time and rate of cooling are decided on concrete steel grade and product effective thickness, wherein: 6～12 ℃/min of heating rate, soaking time 6～15min/mm, air cooling is to room temperature.
2) process annealing is carried out after the homogenizing annealing cooling at supercritical steel, and its temperature value should be controlled at Ac
3About+60～150 ℃.Quickly heat up to the process annealing temperature, insulation regular hour postcooling.Heating rate, soaking time and rate of cooling are decided on concrete steel grade and product effective thickness, wherein: 6～12 ℃/min of heating rate, soaking time 2～6min/mm, air cooling is to room temperature.
Embodiment 1:
In vacuum induction furnace, carry out alloy smelting by the composition in the table 1, smelt the ingot casting that is cast into φ 90mm * 200mm after finishing.This ingot casting cuts into the little ingot casting of φ 90mm * 100mm through electric saw etc.This two little ingot casting is opened forging after the isothermal 3h in 1150 ℃ box-type furnace, be processed into pole and the 15mm * 15mm square rod that sectional dimension is φ 15mm respectively through jumping-up, pulling technology, the two all is cut into cylindrical coupon and 15mm * 15mm * 70mm square column type coupon that size is respectively φ 15mm * 70mm then, uses for follow-up thermal treatment process.Adopt same heat cylindrical and square column type coupon to be carried out the process annealing of air cooling behind the homogenizing annealing of air cooling behind 1100 ℃ of insulation 2h and the 920 ℃ of insulation 1h.A part that cuts coupon is carried out metallographic structure analysis, and metallographic structure and grain-size are seen Fig. 2 respectively.Same batch coupon carries out modifier treatment, is processed into the stretching that complies with the national standard requirements then, impacts that coupon is done mechanical property test and mechanical property test the results are shown in Table 4.Experimental result shows that the tissue that the invention enables supercritical steel to obtain comparatively tiny crystal grain (≤10 μ m) and had good uniformity meanwhile, has obtained good comprehensive mechanical properties, especially impelling strength.In addition, the thermal treatment process of thermal treatment crystal grain thinning of the present invention (homogenizing annealing and process annealing) is all carried out in box high temperature experimental furnace, and the control accuracy of furnace can reach ± and 3 ℃.
Embodiment 2:
In vacuum induction furnace, carry out alloy smelting by the composition in the table 2, smelt the ingot casting that is cast into φ 90mm * 200mm after finishing.This ingot casting cuts into the little ingot casting of φ 90mm * 100mm through electric saw etc.This two little ingot casting is opened forging after the isothermal 3h in 1150 ℃ box-type furnace, be processed into pole and the 15mm * 15mm square rod that sectional dimension is φ 15mm respectively through jumping-up, pulling technology, the two all is cut into cylindrical coupon and 15mm * 15mm * 70mm square column type coupon that size is respectively φ 15mm * 70mm then, uses for follow-up thermal treatment process.Adopt same heat cylindrical and square column type coupon to be carried out the process annealing of air cooling behind the homogenizing annealing of air cooling behind 1080 ℃ of insulation 3h and the 980 ℃ of insulation 1h.A part that cuts coupon is carried out metallographic structure analysis, and metallographic structure and grain-size are seen Fig. 3.Same batch coupon carries out modifier treatment, is processed into the stretching that complies with the national standard requirements then, impacts that coupon is done mechanical property test and mechanical property test the results are shown in Table 4.Experimental result shows that the tissue that the invention enables supercritical steel to obtain comparatively tiny crystal grain (≤10 μ m) and had good uniformity meanwhile, has obtained good comprehensive mechanical properties, especially impelling strength.In addition, the thermal treatment process of thermal treatment crystal grain thinning of the present invention (homogenizing annealing and process annealing) is all carried out in box high temperature experimental furnace, and the control accuracy of furnace can reach ± and 3 ℃.
Embodiment 3:
In vacuum induction furnace, carry out alloy smelting by the composition in the table 3, smelt the ingot casting that is cast into φ 90mm * 200mm after finishing.This ingot casting cuts into the little ingot casting of φ 90mm * 100mm through electric saw etc.This two little ingot casting is opened forging after the isothermal 3h in 1150 ℃ box-type furnace, be processed into pole and the 15mm * 15mm square rod that sectional dimension is φ 15mm respectively through jumping-up, pulling technology, the two all is cut into cylindrical coupon and 15mm * 15mm * 70mm square column type coupon that size is respectively φ 15mm * 70mm then, uses for follow-up thermal treatment process.Adopt same heat cylindrical and square column type coupon to be carried out the process annealing of air cooling behind the homogenizing annealing of air cooling behind 1050 ℃ of insulation 3h and the 950 ℃ of insulation 1h.A part that cuts coupon is carried out metallographic structure analysis, and same batch coupon carries out modifier treatment, is processed into the stretching that complies with the national standard requirements then, impacts that coupon is done mechanical property test and mechanical property test the results are shown in Table 4.Experimental result shows that the tissue that the invention enables supercritical steel to obtain comparatively tiny crystal grain (≤10 μ m) and had good uniformity meanwhile, has obtained good comprehensive mechanical properties, especially impelling strength.In addition, the thermal treatment process of thermal treatment crystal grain thinning of the present invention (homogenizing annealing and process annealing) is all carried out in box high temperature experimental furnace, and the control accuracy of furnace can reach ± and 3 ℃.
Table 1
*Chemical ingredients (massfraction, %)
| Element | C | Si | Mn | P | S | Cr | Mo |
| Become sub specification | 0.09～0.13 | 0.10～0.50 | 0.30～0.60 | ≤0.015 | ≤0.007 | 10.0～11.0 | 1.00～1.20 |
| The coupon composition | 0.11 | 0.25 | 1.13 | 0.01 | 0.007 | 10.20 | 1.03 |
| Element | W | V | Nb | N | Ni | Al | Fe |
| Become sub specification | 1.00～20 | 0.15～0.25 | 0.040～0.080 | 0.040～0.060 | 0.60～0.80 | ≤0.010 | bal. |
| The coupon composition | 1.02 | 0.25 | 0.068 | 0.043 | 0.74 | 0.01 | bal. |
*The Ac of this composition
3It is 861 ℃.
Table 2
*Chemical ingredients (massfraction, %)
| Element | C | Si | Mn | P | S | Cr | Mo |
| Become sub specification | 0.09～0.13 | 0.10～0.50 | 0.30～0.60 | ≤0.015 | ≤0.007 | 10.0～11.0 | 1.00～1.20 |
| The coupon composition | 0.10 | 0.23 | 0.82 | 0.012 | 0.005 | 10.32 | 1.12 |
| Element | W | V | Nb | N | Ni | Al | Fe |
| Become sub specification | 1.00～1.20 | 0.15～0.25 | 0.040～0.080 | 0.040～0.060 | 0.60～0.80 | ≤0.010 | bal. |
| The coupon composition | 1.12 | 0.22 | 0.078 | 0.046 | 0.72 | 0.01 | bal. |
*The Ac of this composition
3It is 887 ℃.
Table 3
*Chemical ingredients (massfraction, %)
| Element | C | Si | Mn | P | S | Cr | Mo |
| Become sub specification | 0.09～0.13 | 0.10～0.50 | 0.30～0.60 | ≤0.015 | ≤0.007 | 10.0～11.0 | 1.00～1.20 |
| The coupon composition | 0.12 | 0.30 | 1.16 | 0.011 | 0.006 | 11.0 | 1.20 |
| Element | W | V | Nb | N | Ni | Al | Fe |
| Become sub specification | 1.00～1.20 | 0.15～0.25 | 0.040～0.080 | 0.040～0.060 | 0.60～0.80 | ≤0.010 | bal. |
| The coupon composition | 1.20 | 0.15 | 0.063 | 0.060 | 0.60 | 0.01 | bal. |
*The Ac of this composition
3It is 876 ℃.
Table 4 mechanical property test result
| Performance index | Tensile strength (MPa) | Yield strength (MPa) | Unit elongation % | Relative reduction in area % | Xia Shi V-type impelling strength (Jcm -2) |
| Embodiment 1 | 818.26 | 655.32 | 23.8 | 69.33 | 235.51 |
| Embodiment 2 | 827.26 | 672.29 | 23.2 | 67.31 | 211.09 |
| Embodiment 3 | 837.60 | 669.92 | 21.2 | 67.77 | 189.38 |
Claims (3)
1, a kind of crystal fining method of supercritical steel is characterized in that: at first when smelting, the composition of supercritical steel is controlled or finely tuned, after supercritical steel carries out homogenizing annealing, adopt the intermediate annealing process crystal grain thinning then; Process for refining may further comprise the steps:
A, according to the one-tenth sub specification of supercritical steel, wherein Mn and Nb element are controlled and are finely tuned;
One-tenth sub specification according to supercritical steel is increased to massfraction 0.8～1.2% to the content of Mn element; Meanwhile, guarantee that the content of Nb element is into the upper limit of sub specification, massfraction 0.06～0.08%;
B, supercritical steel form after the hot-work, and it is carried out homogenizing annealing;
C, supercritical steel carry out process annealing to it after the homogenizing annealing cooling, air cooling to room temperature obtains the original austenite grains of size below 10 μ m then.
2, the crystal fining method of supercritical steel according to claim 1 is characterized in that: among the step b, the homogenizing annealing temperature is controlled at approaching but is not more than a large amount of dissolved temperature of fine precipitated phase MX, and temperature range is: 1020～1100 ℃.
3, the crystal fining method of supercritical steel according to claim 1 is characterized in that: among the step c, the process annealing temperature is a little more than the Chernoff b point of the supercritical steel after Composition Control or the fine setting, and temperature range is: Ac
3+ (60～150) ℃.
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| CN101781743A (en) * | 2010-02-26 | 2010-07-21 | 山西太钢不锈钢股份有限公司 | Seamless steel tube for ultra supercritical boiler and manufacturing method thereof |
| CN104537253A (en) * | 2015-01-07 | 2015-04-22 | 西北工业大学 | Microcosmic phase field analysis method in age forming and pre-ageing process |
| CN108998638A (en) * | 2018-09-13 | 2018-12-14 | 天津重型装备工程研究有限公司 | A kind of heat treatment method of 620 DEG C or more supercritical turbine casting |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| JP3439197B2 (en) * | 2001-03-06 | 2003-08-25 | 三菱重工業株式会社 | Low alloy heat resistant steel, heat treatment method thereof, and turbine rotor |
| JP4386364B2 (en) * | 2005-07-07 | 2009-12-16 | 株式会社日立製作所 | Steam turbine piping, its manufacturing method, main steam piping and reheat piping for steam turbine and steam turbine power plant using the same |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN101781743A (en) * | 2010-02-26 | 2010-07-21 | 山西太钢不锈钢股份有限公司 | Seamless steel tube for ultra supercritical boiler and manufacturing method thereof |
| CN104537253A (en) * | 2015-01-07 | 2015-04-22 | 西北工业大学 | Microcosmic phase field analysis method in age forming and pre-ageing process |
| CN104537253B (en) * | 2015-01-07 | 2017-12-15 | 西北工业大学 | A kind of microcosmic phase field analysis method of age forming preageing process |
| CN108998638A (en) * | 2018-09-13 | 2018-12-14 | 天津重型装备工程研究有限公司 | A kind of heat treatment method of 620 DEG C or more supercritical turbine casting |
| CN114457228A (en) * | 2021-04-02 | 2022-05-10 | 中国科学院金属研究所 | Method for regulating and controlling tissue uniformity of austenitic steel seamless tube |
| CN114457228B (en) * | 2021-04-02 | 2023-06-27 | 中国科学院金属研究所 | Method for regulating and controlling tissue uniformity of austenitic steel seamless tube |
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Application publication date: 20080827 Assignee: HENGDIAN GROUP INNUOVO ELECTRIC CO., LTD. Assignor: Institute of metal research, Chinese Academy of Sciences Contract record no.: 2014330000009 Denomination of invention: Grain refining method for ultra-supercritical steel Granted publication date: 20091021 License type: Common License Record date: 20140120 |
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