CN101831535B - Heat treatment method after forging of ultra-supercritical high and medium pressure rotor steel - Google Patents
Heat treatment method after forging of ultra-supercritical high and medium pressure rotor steel Download PDFInfo
- Publication number
- CN101831535B CN101831535B CN 200910056943 CN200910056943A CN101831535B CN 101831535 B CN101831535 B CN 101831535B CN 200910056943 CN200910056943 CN 200910056943 CN 200910056943 A CN200910056943 A CN 200910056943A CN 101831535 B CN101831535 B CN 101831535B
- Authority
- CN
- China
- Prior art keywords
- forging
- heat treatment
- stove
- treatment method
- rotor steel
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Images
Landscapes
- Forging (AREA)
Abstract
The invention discloses a heat treatment method after forging of ultra-supercritical high and medium pressure rotor steel. The heat treatment after forging of ultra-supercritical high and medium pressure unit rotor steel X12CrMoWVNbN10-1-1 and Cr10.5Mo1W1NiVNbN is carried out by the steps of: step 1. austenite homogenization treatment; step 2. carrying out structural transformation when balanced structure transformation temperature is reached by air cooling; step 3. overall structure softening; and step 4. cooling in a speed limit furnace till discharging. Since the rotor steel is directly put into the furnace for austenization after being forged, the invention has the advantages of short time and good austenite effect, not only eliminates the forging stress, but realizes the homogenization of inner and outer structures of forging. The heat treatment method after forging has the advantages of simple operation, low cost and low energy consumption, and can meet the property requirement of workpieces.
Description
Technical field
The present invention relates to a kind of thermal treatment process, be specifically related to a kind of heat treatment method after forging of ultra supercritical high pressure rotor steel.
Background technology
For large section, large-tonnage ultra supercritical high pressure rotor steel, traditional forging post-heat-treated technology, as shown in Figure 1; When being air cooling to 680 after forging～780 ℃, the 690 ℃ of stoves to be expected of packing into, then 690 ℃ down insulation carried out structural transformation in 200 hours; Be chilled to 240 ℃ with≤8 ℃/h stove again; Insulation fully changes, and being raised to 720 ℃ of insulations again, to carry out organized whole after 22 hours softening, and last stove is cold to be chilled to 180 ℃ with≤8 ℃/h stove and to accomplish and forge post-heat-treated.
Forging by above art breading can be guaranteed the machining cutting ability, but its crystal grain is thick, and the flaw detection reduction coefficient does not reach the flaw detection requirement, and inside appears netted or rolls into a ball cotton-shaped " type troostite " tissue, influences the workpiece performance.Research shows that this is owing to do not carry out processing of austenite homogenizing and directly cooling back isothermal transformation after forging, and organizes grain fineness number uneven thereby cause to cause, and inside and outside composition difference is big, and mixed crystal phenomenon is serious.Therefore, the workpiece that adopts this art breading to come out is difficult to through detecting.
Summary of the invention
Technical problem to be solved by this invention provides a kind of heat treatment method after forging of ultra supercritical high pressure rotor steel, and it can make the inside and outside tissue of forging reach homogenizing.
For solving the problems of the technologies described above, the technical solution of the heat treatment method after forging of ultra supercritical high pressure rotor steel of the present invention is:
Adopt following method that X12CrMoWVNbN10-1-1 and Cr10.5Mo1W1NiVNbN ultra supercritical unit high pressure rotor steel are forged post-heat-treated:
The first step, austenite homogenizing are handled: after the completion of forging finish-forging, it is 950 ± 10 ℃ stove to be expected that forging is directly put into temperature, rises to 1050 ± 10 ℃ of insulations with the heat-up rate of≤50 ℃/h, and soaking time is 0.5～1h/100mm.
In second step, air cooling to balanced weave transition temperature carries out structural transformation: 580～620 ℃ of air cooling to forging surface temperatures, after advance stove immediately, Control for Kiln Temperature is at 690 ± 10 ℃, soaking time is 15h/100mm, carries out balanced weave and changes; Be chilled to 240 ℃ ± 10 ℃ insulations with≤8 ℃/h speed limit stove again, soaking time is 2h/100mm, remains tissue and fully changes.
In the 3rd step, organized whole is softening; Speed with≤15 ℃/h rises to 720 ± 10 ℃, and it is softening that insulation 2h/100mm carries out organized whole.
In the 4th step, the speed limit stove is chilled to comes out of the stove.Be chilled to≤180 ℃ of completion forging post-heat-treated of coming out of the stove with≤8 ℃/h speed limit stove.
The technique effect that the present invention can reach is:
The present invention carries out austenitizing through directly advancing stove after forging, and the time is short, and austenitizing is effective, has not only eliminated forging stress, and makes the inside and outside tissue of forging reach homogenizing.
The present invention is simple to operate, and cost reduces, and energy consumption is few, can satisfy the performance of workpiece requirement.
Description of drawings
Below in conjunction with accompanying drawing and embodiment the present invention is done further detailed explanation:
Fig. 1 is the heat treatment method after forging of prior art ultra supercritical high pressure rotor steel;
Fig. 2 is the heat treatment method after forging of ultra supercritical high pressure rotor steel of the present invention.
Embodiment
As shown in Figure 2, the heat treatment method after forging of ultra supercritical high pressure rotor steel of the present invention, adopt following method that X12CrMoWVNbN10-1-1 and Cr10.5Mo1W1NiVNbN ultra supercritical unit high pressure rotor steel are forged post-heat-treated:
The first step, the austenite homogenizing is handled: forging finish-forging completion back (this moment, the forging temperature was about 900 ℃, about 1000 ℃ of heart portion temperature); Do not carry out air cooling; It is 950 ± 10 ℃ stove to be expected that forging is directly put into temperature, rises to 1050 ± 10 ℃ of insulations with the heat-up rate of≤50 ℃/h, and soaking time is that 0.5～1h/100mm (promptly is the forging insulation 0.5～1 hour of 100mm for diameter; Then be the forging insulation 6～12 hours of 1200mm) for diameter; Carry out the austenite structure homogenizing and handle, eliminate forging stress, adjustment grain fineness number and homogeneous austenite structure are to obtain good matrix;
In second step, air cooling to balanced weave transition temperature carries out structural transformation: 580～620 ℃ of air cooling to forging surface temperatures, after advance stove immediately, Control for Kiln Temperature is at 690 ± 10 ℃, soaking time is 15h/100mm, carries out balanced weave and changes; Be chilled to 240 ℃ ± 10 ℃ insulations with≤8 ℃/h speed limit stove again, soaking time is 2h/100mm, remains tissue and fully changes.
In the 3rd step, organized whole is softening: after insulation finishes, rise to 720 ± 10 ℃ with the speed of≤15 ℃/h, it is softening that insulation 2h/100mm carries out organized whole;
In the 4th step, the speed limit stove is chilled to comes out of the stove: be chilled to≤180 ℃ of completion forging post-heat-treated of coming out of the stove with≤8 ℃/h speed limit stove.
Because being incubated about 12 hours crystal grain down 1040 ℃ of material temperature, this steel grade can not aggravate to grow up; The present invention takes all factors into consideration the furnace temperature and the warm temperature difference of material; And factors such as the cross section of forging, final forging temperature, confirm that finally furnace temperature is 1050 ± 10 ℃, soaking time is 0.5～1h/100mm.
The present invention has abandoned and has forged the cold traditional technology method of laggard line space, but the forging after the finish-forging completion is directly put into 950 ± 10 ℃ high temperature stove to be expected, it is warming up to 1050 ± 10 ℃; Made full use of waste heat after the forging of forging, not only can save energy, and can reach holding temperature in the short period of time; Make internal and external temperature reach consistent, thereby eliminated forging stress, make recrystallize abundant; The insulation short period after the intensification can obtain austenite structure uniformly; Adjusted grain fineness number, had laid a good foundation, made the first thermal treatment UT detect qualification rate and improve for the acquisition of follow-up balanced weave; Can satisfy the flaw detection requirement, prepare for later property heat treatment performs tissue.
Claims (4)
1. the heat treatment method after forging of a ultra supercritical high pressure rotor steel is characterized in that, adopts following method that X12CrMoWVNbN10-1-1 and Cr10.5Mo1W1NiVNbN ultra supercritical unit high pressure rotor steel are forged post-heat-treated:
The first step, the austenite homogenizing is handled; The austenite homogenising treatment method of the said the first step is, after the completion of forging finish-forging, it is 950 ± 10 ℃ stove to be expected that forging is directly put into temperature, rises to 1050 ± 10 ℃ of insulations with the heat-up rate of≤50 ℃/h, and soaking time is 0.5～1h/100mm;
In second step, air cooling to balanced weave transition temperature carries out structural transformation;
In the 3rd step, organized whole is softening;
In the 4th step, the speed limit stove is chilled to comes out of the stove.
2. the heat treatment method after forging of ultra supercritical high pressure rotor steel according to claim 1; It is characterized in that: the method in said second step is; 580～620 ℃ of air cooling to forging surface temperatures, after advance stove immediately, Control for Kiln Temperature is at 690 ± 10 ℃; Soaking time is 15h/100mm, carries out balanced weave and changes; Be chilled to 240 ℃ ± 10 ℃ insulations with≤8 ℃/h speed limit stove again, soaking time is 2h/100mm, remains tissue and fully changes.
3. the heat treatment method after forging of ultra supercritical high pressure rotor steel according to claim 1 is characterized in that: the method in said the 3rd step is, rises to 720 ± 10 ℃ with the speed of≤15 ℃/h, and it is softening that insulation 2h/100mm carries out organized whole.
4. the heat treatment method after forging of ultra supercritical high pressure rotor steel according to claim 1 is characterized in that: the method in said the 4th step is to be chilled to≤180 ℃ of completion forging post-heat-treated of coming out of the stove with≤8 ℃/h speed limit stove.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN 200910056943 CN101831535B (en) | 2009-03-12 | 2009-03-12 | Heat treatment method after forging of ultra-supercritical high and medium pressure rotor steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN 200910056943 CN101831535B (en) | 2009-03-12 | 2009-03-12 | Heat treatment method after forging of ultra-supercritical high and medium pressure rotor steel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN101831535A CN101831535A (en) | 2010-09-15 |
| CN101831535B true CN101831535B (en) | 2012-10-03 |
Family
ID=42715753
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN 200910056943 Active CN101831535B (en) | 2009-03-12 | 2009-03-12 | Heat treatment method after forging of ultra-supercritical high and medium pressure rotor steel |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN101831535B (en) |
Families Citing this family (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103088199B (en) * | 2011-11-04 | 2014-12-24 | 上海重型机器厂有限公司 | Heat treatment method after forging for forged steel bearing roller used for large heavy plate mill |
| CN103131964B (en) * | 2013-03-26 | 2014-11-12 | 上海交通大学 | Method for improving as-cast structure homogeneity of X12CrMoWVNbN10-1-1 martensitic stainless steel |
| CN103667624B (en) * | 2013-08-27 | 2015-09-30 | 内蒙古北方重工业集团有限公司 | High temperature blade steel 1Cr12Ni3Mo2VN step type cooling method for annealing |
| CN107400761B (en) * | 2016-05-20 | 2019-02-12 | 上海电气上重铸锻有限公司 | The heat treatment method of advanced ultra supercritical rotor forging |
| CN106119486A (en) * | 2016-08-30 | 2016-11-16 | 四川六合锻造股份有限公司 | A kind of heat treatment method after forging of ultra-supercritical turbine blade steel |
| CN106929653B (en) * | 2017-03-01 | 2019-05-07 | 上海电气上重铸锻有限公司 | A kind of 25Cr2Ni2MoV rotor made of steel forging heat treatment method after forging |
| CN107598067B (en) * | 2017-09-18 | 2019-02-12 | 无锡宏达重工股份有限公司 | A kind of processing technology of X12CrMoWVNbN10 stator blade ring forging |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101323901A (en) * | 2007-06-12 | 2008-12-17 | 上海重型机器锻件厂 | Austenitic stainless steel as-forged solid solution treatment process after forging |
-
2009
- 2009-03-12 CN CN 200910056943 patent/CN101831535B/en active Active
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101323901A (en) * | 2007-06-12 | 2008-12-17 | 上海重型机器锻件厂 | Austenitic stainless steel as-forged solid solution treatment process after forging |
Non-Patent Citations (2)
| Title |
|---|
| 中国机械工程学会热处理专业分会《热处理手册》编委会.超临界高中压不锈钢转子的热处理.《热处理手册》.机械工业出版社,2001,第2卷574页. * |
| 马力深等.超超临界高中压转子钢TR1200热处理参数与机械性能的研究.《第十届全国塑性工程学术年会、第三届国际塑性加工先进技术研讨会论文集》.2007,626-629. * |
Also Published As
| Publication number | Publication date |
|---|---|
| CN101831535A (en) | 2010-09-15 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101831535B (en) | Heat treatment method after forging of ultra-supercritical high and medium pressure rotor steel | |
| CN107138660B (en) | A kind of high-carbon-chromium bearing steel warm-rolling loop forming method for realizing tissue nodularization | |
| CN103290192A (en) | Thermal treatment process of spliced-welding type large tube plate forging of pressure container | |
| CN103341583B (en) | The forging method of super two-phase stainless steel large-sized tube sheet forging | |
| CN103305672A (en) | Heat treatment process for ultra-large type tube plate forge piece of pressure container | |
| CN102776335A (en) | Process for manufacturing 17-4PH Martensite precipitation-hardening stainless steel forgings | |
| CN104593573A (en) | Combined thermomechanical treatment strengthening method for efficiently improving strength and toughness of non-quenched and tempered steel | |
| CN106929653B (en) | A kind of 25Cr2Ni2MoV rotor made of steel forging heat treatment method after forging | |
| CN106048152B (en) | A kind of heat treatment method improving bar low-temperature impact toughness | |
| CN102399967B (en) | Heat treatment method of eliminating overheated structure of crankshaft forging for large-scale ship | |
| CN110756616B (en) | Preparation method for reducing high-carbon martensitic stainless steel pipe | |
| CN104789748A (en) | Bearing steel tube spheroidizing annealing method | |
| CN100590210C (en) | Technological process for improving twin boundary amount in gamma' precipitation strengthened type ferrous alloy | |
| CN104630443B (en) | Large-scale cylindrical shell section heat treatment method | |
| CN103849745A (en) | Post-forging thermal treatment method for heavy forging of hot-wall hydrogenation reactor | |
| CN101012494A (en) | Method for preparing superfine multiple-phase structure high-carbon steel | |
| CN104962705A (en) | Isothermal normalizing treatment technique of wind power flange | |
| CN107400761B (en) | The heat treatment method of advanced ultra supercritical rotor forging | |
| CN104775009A (en) | Heating method during quenching of large supporting roller | |
| CN103343212B (en) | Heat treatment process after forging of ultra-heavy tube plate forgings splicing-welded in pressure container | |
| CN105296729A (en) | Method for refining Chinese low-activation ferrite-martensite steel grains | |
| CN114369702A (en) | Quenching method of Cr12 roller | |
| CN103572022B (en) | Heat-treatment method for H13 section steel | |
| CN102251089B (en) | Heat treatment method for full diameter 30Cr2Ni4MoV low pressure rotor | |
| CN106399655A (en) | Method for refining ferritic structure by loading microstress on 20MnSi thread steel |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| ASS | Succession or assignment of patent right |
Owner name: SHANGHAI HEAVY MACHINES PLANT CO., LTD. Free format text: FORMER OWNER: SHANGHAI HEAVY-DUTY MACHINERY FORGE PART FACTORY Effective date: 20120702 Free format text: FORMER OWNER: SHANGHAI HEAVY MACHINES PLANT CO., LTD. Effective date: 20120702 |
|
| C41 | Transfer of patent application or patent right or utility model | ||
| TA01 | Transfer of patent application right |
Effective date of registration: 20120702 Address after: 200245 Jiangchuan Road, Shanghai, No. 1800, No. Applicant after: Shanghai Heavy Machines Plant Co., Ltd. Address before: 200245 Jiangchuan Road, Shanghai, No. 1800, No. Applicant before: Shanghai Heavy Machin Forging Factory Co-applicant before: Shanghai Heavy Machines Plant Co., Ltd. |
|
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| C41 | Transfer of patent application or patent right or utility model | ||
| TR01 | Transfer of patent right |
Effective date of registration: 20161206 Address after: 200245 Jiangchuan Road, Shanghai, No. 207, building 1800, No. Patentee after: Shanghai Electric Heavy Forging Co. Ltd. Patentee after: Shanghai Heavy Machines Plant Co., Ltd. Address before: 200245 Jiangchuan Road, Shanghai, No. 1800, No. Patentee before: Shanghai Heavy Machines Plant Co., Ltd. |