CN100408813C - High temperature structural body - Google Patents
High temperature structural body Download PDFInfo
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- CN100408813C CN100408813C CNB2006101420142A CN200610142014A CN100408813C CN 100408813 C CN100408813 C CN 100408813C CN B2006101420142 A CNB2006101420142 A CN B2006101420142A CN 200610142014 A CN200610142014 A CN 200610142014A CN 100408813 C CN100408813 C CN 100408813C
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Abstract
The object of the present invention is to provide a structure for high temperature service in which creep deformation in a medium-temperature low-stress region (temperature range of about 450 to 550 DEG C, stress range of about 10 kg/mm<2>or below) is decreased. For specific aspect, the present invention provides a structure for high temperature, it is characterized in that: a low-alloy steel containing, by mass, 0.05 to 0.17% C, 1.00 to 2.50% Cr and 0.45 to 1.10% Mo is heated to 800 to 1,000 DEG C, then the anneal process can be actualized, said anneal process is cooling down the temperature to at least <=600 DEG C at <=10 DEG C/min cooling rate.
Description
Technical field
The present invention relates to high temperature structural body.Particularly, the present invention relates in middle temperature low stress area (the serviceability temperature scope: about 450～550 ℃, applied stress scope: about 10kg/mm
2Below) have high creep strain repellence high temperature structural body.
Background technique
In the past, as being used for the example of thermal power generation with the refractory steel of steam turbine etc., mainly use low alloy steel (Cr-Mo-V steel, 2.25Cr-Mo steel, Cr-Mo steel) or high Cr steel (9Cr steel, 12Cr steel (and with reference to the spy open clear 60-165359 communique, the spy opens clear 62-103345 communique)).
Wherein, the hot strength of low alloy steel is between carbon steel and high Cr steel, and impact characteristics, weldability are good, and the manufacturing of large-scale forged steel, the former material of cast steel is also very good, and very big competitive ability is also arranged on cost.Therefore, be middle warm area about 450～550 ℃ particularly in the serviceability temperature scope, can preferably use as the turbine construction element.As the low alloy steel of turbine construction element, in the past, by forging, after rolling or cast form be the former material of compound shape simultaneously, can implementing suitable modified heat treatment in order to satisfy the strength characteristics of stipulating.For example, for the former material of the rotor that requires tensile strength characteristics, quenching+temper manufacturing that enforcement is undertaken by chilling for slab, main valve or foundry goods, is implemented normalizing+temper manufacturing of being undertaken by air cooling.
Summary of the invention
When using as the dividing plate of the vapor stream that is used to adjust steam turbine with the slab of the low alloy steel of said method manufacturing or forged steel goods, because as the middle temperature low stress area of target (the serviceability temperature scope: about 450～550 ℃, applied stress scope: about 10kg/mm
2Below) the creep strain amount big, take place so axial creep is crooked ageingly, the result produces dividing plate and contacts with the undesired of rotor.
The present invention is in order to solve above-mentioned problem, and purpose is, the high temperature structural body of the creep strain of warm low stress zones in reducing is provided.
The invention provides a kind of high temperature structural body, it is characterized by, be the low alloy steel of the Mo of the Cr of the C, 1.00～2.50 quality % that contain 0.05～0.17 quality % and 0.45～1.10 quality %, its bainite phase area rate is below 40%, and has ferrite/pearlitic structrure.
The preferred 2.25%Cr-1%Mo steel of above-mentioned low alloy steel, the Mn of the Cr of its C by 0.05～0.15 quality %, 2.00～2.50 quality %, the Mo of 0.90～1.10 quality %, 0.30～0.60 quality %, Si and the surplus of 0～0.50 quality % are formed, and surplus contains Fe and unavoidable impurities element.
In addition, the present invention also provides a kind of high temperature structural body, it is characterized by, the low alloy steel that will contain the Mo of the Cr of C, 1.00～2.50 quality % of 0.05～0.17 quality % and 0.45～1.10 quality % is heated to 800～1000 ℃, implement annealing in process then, described annealing in process is to be cooled at least below 600 ℃ with the rate of cooling below 10 ℃/minute.Especially preferably make rate of cooling below 40 ℃/hour (0.67 ℃/minute).
The preferred 2.25%Cr-1%Mo steel of above-mentioned low alloy steel, the Mn of the Cr of its C by 0.05～0.15 quality %, 2.00～2.50 quality %, the Mo of 0.90～1.10 quality %, 0.30～0.60 quality %, Si and the surplus of 0～0.50 quality % are formed, and surplus contains Fe and unavoidable impurities element.
The preferred bainite phase area of above-mentioned high temperature structural body rate is 0～40% and has a material of ferrite/pearlite/bainite structure.
Above-mentioned high temperature structural body is preferred for the steam turbine member.
Another aspect of the invention is the manufacture method of high temperature structural body, it is characterized by, comprise following operation: the low alloy steel that will contain the Mo of the Cr of C, 1.00～2.50 quality % of 0.05～0.17 quality % and 0.45～1.10 quality % is heated to 800～1000 ℃, implement annealing in process then, described annealing in process is to be cooled at least below 600 ℃ with the rate of cooling below 10 ℃/minute.Especially preferably make rate of cooling below 40 ℃/hour (0.67 ℃/minute).The preferred 2.25%Cr-1%Mo steel of above-mentioned low alloy steel, the Mn of the Cr of its C by 0.05～0.15 quality %, 2.00～2.50 quality %, the Mo of 0.90～1.10 quality %, 0.30～0.60 quality %, Si and the surplus of 0～0.50 quality % are formed, and surplus contains Fe and unavoidable impurities element.
High temperature structural body of the present invention, by its metal structure of Heat Treatment Control, the creep strain of warm low stress area in can reducing.This structure is as the steam turbine member, can prevent the contacting of stationary part and motion portion, sintering, prevents the depoling of connecting part, in addition, its also can be preferably as the member use of gas turbine, boiler etc.
Description of drawings
Fig. 1 has used the schematic representation of the steam turbine of structure of the present invention with dividing plate.
Fig. 2 is the result by the minimum creep rate of Larsen-Miller parameter arrangement comparative steel and steel of the present invention.
To be expression resolve the relatively figure of comparative steel and the relative crooked amount of the dividing plate of steel of the present invention by the 3 dimension creeps of using creep data to Fig. 3.
Fig. 4 is the figure of the crooked amount of creep of expression dividing plate.
Fig. 5 is the figure that represents crooked relatively amount and the correlation of bainite area ratio mutually.
Embodiment
The present invention uses the low alloy steel of the Mo of the Cr of C, 1.00～2.50 quality % contain 0.05～0.17 quality % and 0.45～1.10 quality %.The surplus of low alloy steel is basis with Fe in fact, contains unavoidable impurities usually.As low alloy steel,, still be not subjected to these restriction especially preferably at the hot strength of middle warm area (450～550 ℃), the 2.25%Cr-1%Mo steel of good-toughness.
The 2.25%Cr-1%Mo steel, preferably be made up of the Mn of Mo, 0.30～0.60 quality % of Cr, 0.90～1.10 quality % of C, 2.00～2.50 quality % of 0.05～0.15 quality %, Si and the surplus of 0～0.50 quality %, surplus is made up of Fe and unavoidable impurities element in fact usually.Unavoidable impurities is according to the difference of using raw material and difference, for example can list Nb below 0.035 quality % following P, 0.035 quality % following S, 0.4 quality % following Cu, 0.4 quality % following Ni, 0.03 quality % following V, the 0.02 quality % etc.
Make the 2.25%Cr-1%Mo steel by forging, after rolling, the cast form,, carrying out annealing in process in order to obtain desirable tissue.Annealing in process will keep the regular hour (for example 25mm is corresponding 1 hour) according to thickness of slab under 800～1000 ℃ temperature.At this, when 800 ℃ of treatment temperature less thaies, do not become austenite one phase, therefore the tissue before can not fully destroying can not obtain desirable uniform tissue.In addition, if surpass 1000 ℃, then coarsening, the impact characteristic produces harmful effect.Because can become austenite one phase in the short period of time, and do not worry thickization of crystal grain, so the annealing in process temperature is particularly preferably in about 925 ℃.In addition, heat treated atmosphere can be air atmosphere.
This annealing in process can be implemented in being set at the stove of set point of temperature, because operable device or program are well known by persons skilled in the art, so will not illustrate at this.
Then, the cool condition of annealing in process is to be cooled at least below 600 ℃ in the rate of cooling below 10 ℃/minute with the average cooling rate that is cooled to 600 ℃.This be because, if be cooled to 600 ℃ average cooling rate, then intersects with the ferritic nose of separating out below 10 ℃/minute, can generate a part of ferrite/pearlitic structrure as the present embodiment purpose.And, for the growing amount that makes ferrite/pearlitic structrure increases, rate of cooling is preferred more more slowly, more preferably as below 200 ℃/hour of the cold but speed of stove, be preferably as follows especially and state shown in the embodiment, the control rate of cooling is carried out slow cooling below 40 ℃/hour (0.67 ℃/minute), and if the uncovered temperature of stove is dropped to below 500 ℃, thereby the growing amount of bainite structure is reduced to as far as possible near the zero ferrite/pearlitic structrure that almost all becomes.This is because best rate of cooling should be, and reduces rate of cooling with the separating out of the bainite phase in the control cooling as far as possible, and the rate of cooling that can implement with industrialized mass production equipment.And, the process below annealing in process temperature slow cooling to 600 ℃, also can have rate of cooling be 0 ℃/minute during.That is, at the appointed time, can have do not reduce temperature, remain on uniform temperature during.
In order to finish slow cooling, cool off while can in stove, regulate temperature with the rate of cooling of regulation.
What is called is cooled to be meant below 600 ℃ with the rate of cooling below 10 ℃/minute at least, if be cooled to 600 ℃ with the rate of cooling below 10 ℃/minute, consider that also can cool off with the rate of cooling more than 10 ℃/minute from 600 ℃ to be issued to normal temperature by variation etc. along with the variation of the latitude in season or enforcement place for temperature.From making the viewpoint of efficient, be cooled to below 600 ℃ with the rate of cooling below 10 ℃/minute after, preferred air cooling.
The rate of cooling of control annealing is very important like this be because, can control separating out of bainite phase in the cooling as far as possible, the area ratio of ferrite/pearlitic structrure is improved.Fine needle-like M in ferritic phase
2C type carbide separate out help as the middle temperature low stress area of the service condition of steel of the present invention (the serviceability temperature scope: about 450～550 ℃, applied stress scope: about 10kg/mm
2Below) creep strengthen.Therefore, ferrite/pearlitic structrure has the creep strain repellence higher than bainite structure, so preferably reduce the area ratio of bainite phase as far as possible.
The high temperature structural body that obtains by present embodiment has following feature, control the rate of cooling of annealing in process as mentioned above, make its become the middle temperature low stress area that is adapted at as the service condition of steel of the present invention (the serviceability temperature scope: about 450～550 ℃, applied stress scope: about 10kg/mm
2Below) structural state that uses.
By the high temperature structural body that present embodiment obtains, have in the on-deformable ferrite/pearlitic structrure in middle temperature low stress area.In high temperature structural body of the present invention, what is called has ferrite/pearlitic structrure and is meant, in whole metal structures is ferrite/pearlitic structrure more than 60%, and the area ratio of bainite phase is below 40%.And the mensuration of the area ratio of bainite phase is to calculate by image processing with 100 times observation multiplying power.The high temperature structural body that obtains by normalizing, temper presented the bainite homogeneous structure in the past, though hardness, tensile strength height, have in middle temperature low stress area (the serviceability temperature scope: about 450～550 ℃, applied stress scope: about 10kg/mm
2Below) the big problem of creep strain, and have ferrite/pearlitic structrure by the high temperature structural body that present embodiment obtains, in middle temperature low stress area (the serviceability temperature scope: about 450～550 ℃, applied stress scope: about 10kg/mm
2Below) have a high creep strain repellence.
High temperature structural body of the present invention can preferably use with member as steam turbine.As the steam turbine member, for example can list steam turbine dividing plate, steam turbine unit room, steam turbine clack box, steam turbine main steam line.And, by being applied to the steam turbine dividing plate, can prevent owing to steam turbine contacting with the creep of ageing ground of dividing plate crooked that cause and rotor.In addition, by being applied to the steam turbine unit room, can prevent that creep strain owing to the steam turbine unit room from causing with the contacting of rotary part.In addition, by being applied to the steam turbine clack box, can prevent the sintering of the slide part that causes owing to the ageing ground creep strain of steam turbine clack box.And, by being applied to the steam turbine main steam line, can prevent the depoling of the connecting part that causes owing to the ageing ground creep strain of steam turbine main steam line.
The steam turbine that Fig. 1 has represented to use structure of the present invention is with dividing plate 1 and be provided with the schematic representation of the steam turbine 10 of this dividing plate.In steam turbine 10, dividing plate 1 is installed on the housing 2, and movable vane 3 is installed on the rotor 4.Steam turbine is to adjust the member that vapor stream is delivered to movable vane then with dividing plate 1, is with outer ring and the inner ring structure in conjunction with stator blade.Its in the steam turbine that common firepower is used, in middle temperature low stress area (the serviceability temperature scope: about 450～550 ℃, applied stress scope: about 10kg/mm
2Below) use.And, used the steam turbine dividing plate of structure of the present invention, under such condition, the creep diagonal distortion does not take place yet through about time more than 300,000 hours, high creep resistant is arranged.
In addition, high temperature structural body of the present invention can be used as gas turbine and uses with member, as the gas turbine member, for example can enumerate the outer unit room of gas turbine.And, by being applied to the outer unit room of gas turbine, can prevent since gas turbine ageing ground of unit room creep strain outward cause with the contacting of rotary part.In addition, high temperature structural body of the present invention also can be applied to boiler tubing.And, by being applied to boiler tubing, can prevent the creep strain of ageing ground of boiler tubing.
Embodiment and comparative example
With the 150mm slab of the 2.25%Cr-1%Mo steel (ASTM A387Gr22 steel) of the chemical composition shown in the table 1, implement the heat treatment of condition shown in the table 2, research organization and creep properties.With the air cooling material that the used steel of making comparisons in the past, the rate of cooling stove following with 40 ℃/hour (0.67 ℃/minute) is as cold as 600 ℃, after open furnace carries out air cooling then, test material with the fast skin section of rate of cooling wherein is an invention steel-1, the test material of the central part that rate of cooling is slow is a steel of the present invention-2, and be as cold as 500 ℃ with 40 ℃/hour (0.67 ℃/minute) following rate of cooling stove, after open furnace carries out air cooling then, be steel of the present invention-3 with its skin section.
Table 1
Table 2
Table 3 expression structure observation result.The air cooling material of comparative steel is shown as the bainite homogeneous structure, and in steel of the present invention, the area ratio of bainite phase reduces, and the ratio of ferrite/pearlitic structrure increases.The skin section (steel 1 of the present invention) of the area ratio of bainite phase test material of open furnace by 600 ℃ time the, central part (steel 2 of the present invention), the order of the skin section (steel 3 of the present invention) of the test material of open furnace reduces 500 ℃ the time, and the area ratio of bainite phase roughly depends on rate of cooling as can be known.Zero for bainite is close, the rate of cooling that preferred 40 ℃/hour (0.67 ℃/minute) is following, and below 500 ℃ stove is being opened wide.
Table 3
Fig. 2 represents the result with minimum creep rate in Larsen-Miller parameter (Larson Miller Parameter:LMP) arrangement creep experiments.Larsen-Miller parameter is represented with following formula.
LMP＝(273+T)×(20-logA)/1000
(in the formula, T represents temperature (unit: ℃), and A represents minimum creep rate (unit: mm/mm/Hr).)
By following formula as can be known, the more little LMP of minimum creep rate is big more, so show in Fig. 2 the creep strain speed of turning right more more little (creep strain is little).At stress is 20kg/mm
2The above region of high stress, the creep strain speed of comparative steel is little, and still, the low stress area below that is particularly at 10kg/mm
2Below, order reverses, and the creep strain speed of steel of the present invention is relatively little.That is, demonstrate at 10kg/mm
2Following low stress area, ferrite/pearlitic structrure more helps reducing creep strain speed with respect to bainite structure.Even in steel of the present invention, think that also creep strain rate changes along with the variation of the area ratio of bainite phase, has the tendency that bainite phase area rate is more little, creep strain speed is more little.
Fig. 3 represents to resolve the comparison that the crooked amount of dividing plate is done by the three-dimensional creep of using above-mentioned creep data.At this, the crooked relatively amount of the longitudinal axis, expression is 1 o'clock crooked relatively amount with the crooked amount of comparative steel running after 300000 hours.
The crooked amount of dividing plate (the crooked amount of creep) as shown in Figure 4.Dividing plate is that the outer ring is fixed on the structure on the unit room, with respect to the vapor stream direction in downstream side generation creep strain.The inner ring of this dividing plate is the crooked amount of creep to the amount of downflow direction distortion.In practical measurement,, measure the crooked amount of the end rear flow side of week in the inner ring with the installation base portion of the downstream side reference point before as distortion.
Steel of the present invention is as can be known compared with comparative steel, and the crooked amount of creep is little, and particularly timeliness is with low uncertainty.And, turning round, the crooked relatively amount of steel of the present invention reduces significantly after 300000 hours, be about comparative steel crooked relatively amount 15%～46%, if reduce so far, can positively avoid contacting of rotor and dividing plate in projected life at equipment, the continuous running of the steam turbine of reality is not had obstacle.Therefore, it is very high to have used the steam turbine reliability of dividing plate of the present invention.
The crooked relatively amount after Fig. 5 represents to turn round 300000 hours and the relation of the bainite amount of separating out mutually.The area ratio of bainite phase is big more as can be known, and crooked relatively amount has the tendency of increase more, in order to reach the crooked relatively amount as half of the comparative steel of target, as long as the area ratio of control bainite phase (is comprising zero) 40% below.And, if can reach crooked relatively amount, can avoid contacting of rotor and dividing plate in projected life at equipment as half of the comparative steel of target, make the stable running of steam turbine.
Confirmed that more than if control the rate of cooling of the annealing in process of 2.25%Cr-1%Mo steel, the area ratio of control bainite phase then can reduce crooked relatively amount significantly below 40%.
Claims (9)
1. a high temperature structural body is characterized by, and is the low alloy steel of the Mo of the Cr of the C, 1.00～2.50 quality % that contain 0.05～0.17 quality % and 0.45～1.10 quality %, and its bainite phase area rate is below 40%, and has ferrite/pearlitic structrure.
2. high temperature structural body according to claim 1, wherein, described low alloy steel is by the Si of Mn, 0～0.50 quality % of Mo, 0.30～0.60 quality % of Cr, 0.90～1.10 quality % of C, 2.00～2.50 quality % of 0.05～0.15 quality % and the 2.25%Cr-1%Mo steel that surplus is formed, and this surplus contains Fe and unavoidable impurities element.
3. high temperature structural body, it is characterized by, the low alloy steel that will contain the Mo of the Cr of C, 1.00～2.50 quality % of 0.05～0.17 quality % and 0.45～1.10 quality % is heated to 800～1000 ℃, implement annealing in process then, described annealing in process is to be cooled at least below 600 ℃ with the rate of cooling below 10 ℃/minute.
4. high temperature structural body according to claim 3, wherein, described low alloy steel is by the Si of Mn, 0～0.50 quality % of Mo, 0.30～0.60 quality % of Cr, 0.90～1.10 quality % of C, 2.00～2.50 quality % of 0.05～0.15 quality % and the 2.25%Cr-1%Mo steel that surplus is formed, and this surplus contains Fe and unavoidable impurities element.
5. according to claim 3 or 4 described high temperature structural bodies, bainite phase area rate is below 40%, and has ferrite/pearlitic structrure.
6. the steam turbine member that constitutes by each described high temperature structural body in the claim 1～5.
7. the steam turbine that possesses the described steam turbine member of claim 6.
8. the manufacture method of a high temperature structural body, it is characterized by, comprise following operation: the low alloy steel that will contain the Mo of the Cr of C, 1.00～2.50 quality % of 0.05～0.17 quality % and 0.45～1.10 quality % is heated to 800～1000 ℃, implement annealing in process then, described annealing in process is to be cooled at least below 600 ℃ with the rate of cooling below 10 ℃/minute.
9. the manufacture method of high temperature structural body according to claim 8, wherein, described low alloy steel is by the Si of Mn, 0～0.50 quality % of Mo, 0.30～0.60 quality % of Cr, 0.90～1.10 quality % of C, 2.00～2.50 quality % of 0.05～0.15 quality % and the 2.25%Cr-1%Mo steel that surplus is formed, and in fact this surplus is made up of Fe and unavoidable impurities element.
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| JP2005291829A JP4781767B2 (en) | 2005-10-05 | 2005-10-05 | Manufacturing method of structure for high temperature |
| JP2005291829 | 2005-10-05 |
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| CN112176156A (en) * | 2020-08-26 | 2021-01-05 | 江阴兴澄特种钢铁有限公司 | Production method of SA387Gr22CL2 steel plate for head of pressure-bearing equipment and simulated hot forming method |
Citations (5)
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| CN1265711A (en) * | 1997-07-28 | 2000-09-06 | 埃克森美孚上游研究公司 | Ultra-high strength, weldable, essentially boron-free steels with superior toughness |
| JP2004143593A (en) * | 2002-10-01 | 2004-05-20 | Sumitomo Metal Ind Ltd | High strength seamless steel tube having excellent hydrogen induced cracking resistance, and production method therefor |
| JP2004169055A (en) * | 2002-11-15 | 2004-06-17 | Aichi Steel Works Ltd | Age hardening type high-strength bainitic steel parts superior in machinability and manufacturing method therefor |
| JP2005133152A (en) * | 2003-10-30 | 2005-05-26 | Kobe Steel Ltd | High-strength wire rod to be induction-hardened superior in cold workability and impact resistance, and steel component using the wire rod |
| US20050167013A1 (en) * | 2002-10-01 | 2005-08-04 | Nobutoshi Murao | High strength seamless steel pipe excellent in hydrogen-induced cracking resistance and its production method |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS57143467A (en) * | 1981-02-27 | 1982-09-04 | Kawasaki Steel Corp | Low c-low si-cr-mo steel used in wet vapor |
| JPH01162724A (en) * | 1987-12-21 | 1989-06-27 | Kawasaki Steel Corp | Manufacture of high strength cr-mo steel pipe having superior corrosion resistance and weldability |
| JPH07324601A (en) * | 1994-05-31 | 1995-12-12 | Mitsubishi Heavy Ind Ltd | Diaphragm structure for steam turbine |
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2005
- 2005-10-05 JP JP2005291829A patent/JP4781767B2/en active Active
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- 2006-09-30 CN CNB2006101420142A patent/CN100408813C/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1265711A (en) * | 1997-07-28 | 2000-09-06 | 埃克森美孚上游研究公司 | Ultra-high strength, weldable, essentially boron-free steels with superior toughness |
| JP2004143593A (en) * | 2002-10-01 | 2004-05-20 | Sumitomo Metal Ind Ltd | High strength seamless steel tube having excellent hydrogen induced cracking resistance, and production method therefor |
| US20050167013A1 (en) * | 2002-10-01 | 2005-08-04 | Nobutoshi Murao | High strength seamless steel pipe excellent in hydrogen-induced cracking resistance and its production method |
| JP2004169055A (en) * | 2002-11-15 | 2004-06-17 | Aichi Steel Works Ltd | Age hardening type high-strength bainitic steel parts superior in machinability and manufacturing method therefor |
| JP2005133152A (en) * | 2003-10-30 | 2005-05-26 | Kobe Steel Ltd | High-strength wire rod to be induction-hardened superior in cold workability and impact resistance, and steel component using the wire rod |
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| JP4781767B2 (en) | 2011-09-28 |
| JP2007100168A (en) | 2007-04-19 |
| CN1944960A (en) | 2007-04-11 |
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Owner name: MITSUBISHI HITACHI POWER SYSTEM LTD. Free format text: FORMER OWNER: MITSUBISHI JUKOGIO KK Effective date: 20150402 |
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Address after: Yokohama, Japan Patentee after: Mitsubishi Power Co., Ltd Address before: Yokohama, Japan Patentee before: MITSUBISHI HEAVY INDUSTRIES, Ltd. |
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