JP4542491B2 - High-strength heat-resistant cast steel, method for producing the same, and uses using the same - Google Patents

Description

  The present invention has a high creep rupture strength and good weldability at 620 ° C. or higher, a main steam temperature and a pressure of 620 ° C. or higher, and a super-critical pressure turbine casing of a super supercritical pressure turbine having a pressure of 25 MPA or higher, and a main steam stopper. The present invention relates to a novel heat-resistant cast steel suitable for a valve and a regulating valve casing, a method for producing the same, a casing for a steam turbine using the same, a main steam stop valve, a steam regulating valve, and a steam turbine power plant.

  In a conventional steam turbine having a steam temperature of 600 ° C. or lower, CrMoV low alloy cast steel or 11CrMoVNb cast steel is used as a casing material. However, from the viewpoint of depletion of fossil fuels such as oil and coal and energy saving, it is desired to improve the power generation efficiency of the steam turbine, and the most effective means is to increase the steam temperature and pressure to improve the power generation efficiency. For this reason, steam power generation is being promoted at higher temperatures. As these high-efficiency turbine materials, the current casing material is insufficient in strength, and a material having higher strength is required.

  As a high-temperature steam turbine casing having a steam temperature of 620 ° C. or higher, the high-temperature strength is insufficient. Patent Document 1 discloses a casing made of 9% CR steel, but showed a variation in high-temperature strength. The conventional steam turbine has a steam temperature of 600 ° C. and a steam pressure of 25 MPa. 1Cr-1Mo-1 / 4V ferritic low alloy forged steel or 11Cr-1Mo-V-Nb-N forged steel as rotor material, 1Cr-1Mo-1 / 4V ferritic low alloy cast steel or 11Cr-1Mo-V- as casing material Nb-N cast steel is known, and as these materials, austenitic alloys shown in Patent Document 2 and martensitic steels shown in Patent Documents 3, 4, and 5 are known as materials having higher high-temperature strength. ing.

JP-A-7-118812 JP 62-180044 A JP-A-2-290950 JP-A-4-371551 Japanese Patent Laid-Open No. 9-59747

As a material having higher high-temperature strength than the above-described conventional casing material, a martensitic cast steel shown in Patent Document 5 is known. However, the strength is insufficient for use as a steam turbine casing having a steam temperature of 620 ° C., and since the wall thickness must be increased, there is a problem of generating a large thermal stress when the turbine is started and stopped.
Although the above-mentioned publications disclose rotor materials and casing materials, the steam turbine and the thermal power plant system associated with higher temperatures are not taken into consideration at all as described above.

An object of the present invention is to provide a high strength heat-resistant cast steel having high creep rupture strength and toughness at 620 ° C. or higher and good weldability, a method for producing the same, a steam turbine casing , a main steam stop valve, and a steam control valve using the same. And a manufacturing method thereof, and a steam turbine and a steam turbine power plant.

The present invention relates to C0. 10 ~0.16%, Si0.1~ 0.6%, Mn0. 3 ~ 0.8%, Cr 9.5 ~1 1.5%, Ni0.1 2 ~ 0.8%, Mo 0.2~ 0.7%, W1.9~3.0%, V0.05 -0.3%, the total amount of one or more of Nb, Ta and Zr is 0.01-0.15%, Co0. A high-strength heat-resistant cast steel containing 2 to 1.5 %, N 0.01 to 0.08% and B 0.0005 to 0.01%, the balance being made of Fe and inevitable impurities, and its use Steam turbine casing, main steam stop valve and steam control valve.

  In the present invention, by mass, Al is 0.0005 to 0.04% and O is 0.02% or less, and orthogonal coordinates represented by the relationship of [W / (Mo + 0.5W)] and (Co / W). The coordinate point A (1.1, 0.90), the coordinate point B (1.5, 0.55), and the coordinate point C (1.8, 0.55) are connected by straight lines. It is preferable to have [W / (Mo + 0.5W)] and (Co / W) that are less than or equal to the values obtained.

  In addition, the present invention preferably contains at least one of Re 1.5% or less, Nd 0.5% or less, and Sr 1.0% or less by mass.

Furthermore, the present invention has a creep rupture strength at 620 ° C. for 10 ⁵ h of 98 MPA or more, an impact absorption energy at room temperature of 29.4 J or more, and good weldability. In order to ensure higher reliability, it is preferable that the creep rupture strength at 620 ° C. and 10 ⁵ h is 108 MPa or more and the room temperature impact absorption energy is 31.4 J or more.

  The method for producing high-strength heat-resistant cast steel according to the present invention is characterized in that the raw materials having the compositions of the heat-resistant cast steels are melted in an electric furnace and cast into a sand mold after degassing by vacuum ladle refining. Then, the cast steel after casting is annealed at 1000 to 1150 ° C., heated to 1000 to 1100 ° C. and rapidly cooled, and then tempered twice in sequence at 550 to 750 ° C. and 670 ° C. to 770 ° C. Is what you do.

  A high-strength heat-resistant cast steel according to the present invention and a steam turbine casing, a main steam stop valve, and a steam control valve using the same have the above composition and are manufactured by the above manufacturing method. The steam turbine casing, a main steam stop valve, and a steam control valve are included. Hereinafter, the reasons for limiting the components of the material of the present invention will be described.

In order to obtain high tensile strength, C is 0. Although the element is necessary for 10 % or more, if it exceeds 0.16%, the metal structure becomes unstable when exposed to high temperature for a long time, and the creep rupture strength is lowered for a long time. It is limited to 10 to 0.16 percent. Especially 0. The range of 10 to 0.14% is preferable, and more preferably 0. A range of 10 to 0.12% is preferred.

Mn is added as a deoxidizing agent. The effect is achieved with the addition of 3 %, and the addition of more than 0.8 % reduces the creep rupture strength. In particular , 0.4 to 0.7% is preferable.

Si is also added as a deoxidizer. According to steelmaking techniques such as vacuum carbon deoxidation, the addition of Si can be reduced, but addition of 0.1% or more is necessary. Further, since Si produces a harmful δ ferrite structure, addition exceeding 0.6 % should be avoided. And, by lowering Si, there is an effect of preventing generation of harmful δ ferrite structure. Therefore, it is necessary to keep the 0.6% or less in the case of addition, good Ri 0.2 to 0.6 percent is preferred.

Cr has the effect of improving high temperature strength and high temperature oxidation. If it exceeds 11.5 %, a harmful δ ferrite structure will be formed, and excessive addition will cause a decrease in toughness. If it is less than 9.5 %, the oxidation resistance against high-temperature and high-pressure steam becomes insufficient. In particular , 10.0 to 11.0% is preferable.

Ni is an element that suppresses the formation of δ ferrite and imparts toughness, and needs to be at least 0.1 2 %. However, if it exceeds 0.8 %, the creep rupture strength at 620 ° C. or higher is reduced. limited to .1 2 to 0.8 percent. In particular, preferably 0.3 to 0.7 percent.

  W has an effect of remarkably increasing the high temperature long time strength. When W is less than 1.9%, the strength improvement effect is insufficient as a heat-resistant cast steel used at 620 ° C. or higher. On the other hand, if W exceeds 3.0%, the toughness becomes low. In particular, it is preferably 1.95 to 2.7%, more preferably 2.0 to 2.5%.

Mo is added by 0.2% or more in order to improve the high temperature strength. However, when it contains W exceeding 1.9% as in the present invention cast steel, addition of Mo exceeding 0.7 % lowers toughness and fatigue strength, so it is limited to 0.7 % or less. In particular, 0.2 to 0.6% is preferable.
V has the effect of increasing the creep rupture strength. If it is less than 0.05%, the effect is insufficient, and if it exceeds 0.3%, δ ferrite is generated and the fatigue strength is lowered. In particular, 0.10 to 0.25%, more preferably 0.12 to 0.23% is preferable.

  Nb is a very effective element for increasing the high-temperature strength. However, when added in a large amount, coarse eutectic NB carbides are generated particularly in large steel ingots, and the strength is reduced or the fatigue strength is reduced. Since it causes δ ferrite to precipitate, it must be suppressed to less than 0.15%. Moreover, the effect is insufficient with NB less than 0.01%. Particularly in the case of a large steel ingot, 0.02 to 0.12% is preferable and 0.04 to 0.10% is more preferable.

  Ta and Zr have an effect of increasing low temperature toughness, and a sufficient effect can be obtained by adding Ta or less and Ta 0.15% or less alone or in combination. When Ta is added in an amount of 0.1% or more, the addition of Nb can be omitted.

Co is 0. Addition of 2 % or more significantly improves the high temperature strength. This is considered to be due to the interaction with W, and is a characteristic phenomenon in the present alloy containing 1.9% or more of W. On the other hand, excessive addition of more than 1.5 % of Co lowers the structure stability at high temperature, and thus decreases the creep rupture strength. It is limited to 2 to 1.5 %. In particular , 0.2 to 1.2% is preferable.

  N precipitates V nitride, and has the effect of increasing the high temperature strength by the IS effect (interaction between interstitial and substitutional solid solution elements) in collaboration with Mo and W in a solid solution state. However, at least 0.01% is necessary, but if it exceeds 0.08%, the ductility is lowered, so it is limited to 0.01 to 0.08%. In particular, 0.015 to 0.075%, more preferably 0.015 to 0.06% is preferable.

Al is added in an amount of 0.0005% or more as a deoxidizing agent and a crystal grain refining agent. Al is a strong nitride forming element, by fixing the nitrogen works effectively to creep, have the effect of reducing the long-term creep strength of at least 10 4 ^h in a high temperature range especially exceeds 0.04%. Further, Al promotes the precipitation of the Laves phase, which is a brittle intermetallic compound mainly composed of W, invites the precipitation to the crystal grain boundary, and lowers the creep rupture strength on the long time side. In particular. In extreme grain refinement, Laves phase is continuously precipitated at grain boundaries. Therefore, the upper limit is made 0.04%. In particular, 0.001 to 0.035%, more preferably 0.003 to 0.030% is preferable.

B is a solid solution in the grain boundary strengthening effect and _M 23 _{C 6,} has the effect of enhancing the high temperature strength by the action preventing the aggregation and coarsening of _M 23 _{C 6} type carbide, it is effective to add a minimum 0.0005% However, if over 0.01%, weldability is impaired, so the content is limited to 0.0005 to 0.01%. In particular, 0.001 to 0.008%, more preferably 0.002 to 0.007% is preferable.

  If the content of O exceeds 0.015%, the high-temperature strength and toughness value are lowered, so it should be 0.020% or less, particularly 0.015% or less, more preferably 0.010% or less.

  In particular, it has been experimentally clarified that Mo, W, and Co are greatly involved in high-temperature strength and high-temperature structure stability and act in a composite manner in the steel of the present invention.

  That is, in order to obtain material properties that have both high-temperature strength and high-temperature structure stability at 620 ° C. or higher, the ratio of Mo and W that improves creep strength is increased, and the W ratio that significantly improves high-temperature long-term strength is increased. In order to improve the high-temperature structure stability, it is preferable to reduce the Co / W addition ratio Co / W. In the relationship between Cartesian coordinates [W / (Mo + 0.5W)] and (Co / W) indicating the relationship among Mo, W and Co, coordinate point A (1.2, 0.80), coordinate point B ( 1.5, 0.55) and the coordinate point C (1.8, 0.55) are preferably shown in the region represented by the straight line ABC or less obtained by connecting the points with straight lines.

  Re significantly increases the high-temperature strength by solid solution strengthening. Excessive addition promotes embrittlement, so addition of 2% or less is preferable, but Re is a rare element, and is practically 1.5% or less, more preferably 1.2% or less.

  Nd increases the high temperature strength by forming carbonitrides. Nd is effective even when added in a small amount. Excessive addition promotes embrittlement, so addition of 1% or less is preferable, but Nd is a rare element and is practically 0.5% or less, more preferably 0.3%. The following is preferred.

  Sr strengthens the prior austenite grain boundaries, increases the low temperature toughness and strength, and in particular increases the creep rupture strength. Excessive addition promotes the formation of carbonitrides at the grain boundaries, makes the grain boundaries brittle and lowers toughness and strength, so 1.0% or less is preferred. Sr is a rare element, and is practically 0.8% or less, more preferably 0.5% or less.

  In the heat-resistant cast steel casing, the main steam stop valve and the steam control valve of the present invention, when the δ ferrite structure is mixed, the high-temperature creep rupture strength and the low-temperature toughness are lowered. Therefore, the structure is preferably a uniform tempered martensite structure. In order to obtain a tempered martensite structure, the Cr equivalent represented by the following formula (1) must be 10 or less. If the Cr equivalent is too low, the high temperature creep rupture strength will decrease, so it must be 4 or more.

Cr equivalent (wt%) = Cr + 6Si + 4Mo + 1.5W + 11V + 5Nb-40C
-30N-30B-2Mn-4Ni-2Co (1)
Further, the reduction of P and S has the effect of increasing the creep rupture strength and low temperature toughness, and it is desirable to reduce it as much as possible. From the viewpoint of improving low temperature toughness, P of 0.020% or less and S of 0.020% or less are preferable. In particular, P is 0.015% or less, S 0.015% or less, more preferably P0.010% or less, and S 0.010% or less.

  Reduction of Sb, Sn and As also has the effect of increasing low temperature toughness, and it is desirable to reduce it as much as possible. However, from the viewpoint of the current steelmaking technology level, Sb is 0.0015% or less, Sn 0.01% or less, and As 0.02%. The following is preferred. Particularly, Sb 0.0010% or less, Sn 0.005% and As 0.01% or less are desirable.

Since the steam turbine casing, the main steam stop valve, and the steam control valve are exposed to high-pressure steam at 620 ° C. or higher, high stress due to internal pressure acts. Therefore, from the viewpoint of preventing creep rupture, the casing material 620 ° C., 10 ⁵ h creep rupture strength is required more than 98 MPa. Further, since thermal stress acts when the member temperature is low when the turbine is started, room temperature impact absorption energy of 29.4 J or more is required from the viewpoint of preventing brittle fracture. In particular, to ensure a higher reliability, 620 ° C., 10 ⁵ h creep rupture strength 103MPa or more, it is preferable that the room temperature impact absorption energy 30.9J more.

  In particular, since the steam turbine casing has a large ingot weight of around 50 tons, a high manufacturing technique is required to produce a steel ingot with few defects. The high-strength heat-resistant cast steel according to the present invention can be made sound by melting an alloy raw material having a target composition in an electric furnace, degassing it by vacuum ladle refining, casting into a sand mold, and molding. By carrying out sufficient refining and deoxidation before casting, the casting defects such as shrinkage can be reduced. The same applies to the main steam stop valve and the steam control valve.

In addition, the formed heat-resistant cast steel is annealed at 1000 to 1150 ° C., then heated to 1000 to 1100 ° C., and quenched rapidly, primary tempering at 550 to 750 ° C., and secondary tempering at 670 to 770 ° C. By carrying out sequentially, large-sized steel ingots, such as a steam turbine casing which can be used in the steam of 620 degreeC or more, can be manufactured. If the annealing and normalizing temperatures are 1000 ° C. or less, the carbonitride cannot be sufficiently dissolved, and if it is too high, crystal grains become coarse. In addition, the tempering twice can completely decompose the retained austenite and make uniform tempered martensite. By manufacturing the above method, 98 MPa or more 620 ° C., 10 and ⁵ hours creep rupture strength, obtained at room temperature impact absorption energy above 29.4J, the steam turbine casing usable in 620 ° C. or higher in the vapor it can.

  According to the present invention, a ferritic heat-resistant cast steel having high 620 ° C. creep rupture strength and room temperature toughness can be obtained, so that it can be used for a casing for an ultra-supercritical steam turbine up to a temperature of 650 ° C.

  By using the heat-resistant cast steel according to the present invention instead of the austenitic heat-resistant cast steel for casings for ultra-supercritical steam turbines up to a temperature of 650 ° C., it can be manufactured with the same design philosophy as in the past, and further the austenitic heat-resistant steel. Since the coefficient of thermal expansion is smaller than that of cast steel, there are advantages such that the rapid start-up of the steam turbine is facilitated and that it is less susceptible to thermal fatigue damage.

  Hereinafter, the best mode for carrying out the present invention will be described in detail by way of specific examples, but the present invention is not limited to these examples.

  Table 1 shows the chemical composition (mass%) of the heat-resistant cast steel according to the present invention. The sample was assumed to be a thick part of a large casing, and 200 kg was melted using a high-frequency induction melting furnace, and cast into a sand mold having a maximum thickness of 200 mm, a width of 380 mm, and a height of 440 mm to produce an ingot. Sample No. 1 to 13 are the materials of the present invention. 30 to 35 are comparative materials as conventional materials. Each sample is assumed to be a thick-walled portion of a large turbine casing after annealing at 1050 ° C. × 8 h for furnace cooling, air cooling normalization after heating at 1050 ° C. × 8 h, and primary cooling at air cooling after holding at 680 ° C. × 7 h. And after heating and holding at 710 ° C. for 7 hours, air-cooled secondary tempering was performed.

Table 2 shows the tensile properties at room temperature, V-notch Charpy impact absorption energy at 20 ° C., 620 ° C. × 10 ⁵ h creep rupture strength, and weld crack test results.

Appropriate amounts of B, Mo, W, and Co are added, and the present material No. Nos. 1 to 13 are characteristics required for a high-temperature and high-pressure turbine casing up to 650 ° C. in terms of creep rupture strength and impact absorption energy (620 ° C. × 10 ⁵ h strength ≧ 98 MPA, 20 ° C. shock absorption energy ≧ 29.4 J). Is sufficiently satisfied.

  FIG. 1 is a diagram showing the relationship between the amount of W added and creep rupture strength for 100,000 hours. As shown in FIG. 32 is 0.057%. 33 is 0.053%. 35 is 0.04%. 34 is 0.04%. 31 is 0.04%. 30 is 0.03%, and in all cases, the creep rupture strength is increased by increasing the W content, and the effect is greater as the Nb content is higher. However, No. having Co of 0.2 to 1.5% of the material of the present invention. It is clear that those of 1 to 13 all have higher creep rupture strength compared to the same Nb amount and the same W amount. Note that when the W amount is 1.8% or less, the influence of the W amount is not observed, but when the W amount is 1.8% or more, the creep rupture strength is remarkably increased. Furthermore, No. of this invention material. In the case of Nos. 1 to 13, the creep rupture strength is remarkably increased by increasing the W amount at the same Nb amount around 0.04% and Nb amount around 0.08%.

  FIG. 2 is a diagram showing the relationship between the W addition amount and the impact absorption energy. As a result of investigating the influence of W on the mechanical properties, it is clear that the impact absorption energy decreases as the W amount increases, as shown for the same Nb amount as described above. However, in the present invention, No. having Co of 0.2 to 1.5%. It is clear that those of 1 to 13 have higher impact absorption energy compared to the same Nb amount and the same W amount. Furthermore, the material of the present invention does not show a reduction in shock absorption energy at room temperature when the W content is within 3.0%. In addition, when the Nb content is as low as 0.03 to 0.06%, there is no reduction in impact absorption energy at room temperature due to an increase in the W content.

FIG. 3 is a diagram showing the relationship between the Co addition amount and the 100,000 hour creep rupture strength. As shown in FIG. 3, it is clear that the creep rupture strength decreases conversely by increasing the Co content at the same Nb content as described above. However, according to the present invention No. having low Co and medium Co having 0.2 to 1.5% Co. In Nos. 1 to 13, the creep rupture strength is increased by increasing the amount of Co. Accordingly, when the Co content is 1.5 % or less, all of them have a higher creep rupture strength. When the Co content exceeds 1.5 %, the creep rupture strength due to the increased Co content is increased by the increase. It is clear that it falls.

FIG. 4 is a diagram showing the relationship between the Co addition amount and the impact absorption energy. As shown in FIG. 4, both the comparative material and the material of the present invention tend to have higher impact absorption energy as the amount of Co increases. However, if it exceeds 1.5 %, the structural stability is lowered and the creep strength is lowered for 10 ⁵ hours as described above, which is not preferable.

  FIG. 5 is a diagram showing the relationship between W / (Mo + 0.5W) and 100,000 hour creep rupture strength. As shown in FIG. In the case of 30 to 35, the increase in W / (Mo + 0.5W) results in a slight decrease in the 100,000-hour creep rupture strength, but the material of the present invention has a 100,000-hour creep rupture strength due to the increase in W / (Mo + 0.5W). It is clear that the height is increased.

  FIG. 6 is a diagram showing the relationship between W / (Mo + 0.5W) and shock absorption energy. As shown in FIG. In 30 to 35, the impact absorption energy is slightly reduced by increasing W / (Mo + 0.5W), but the material of the present invention does not show a decrease in impact absorption energy by increasing W / (Mo + 0.5W). Is clear.

  FIG. 7 is a diagram showing the relationship between (Co / W) and 100,000-hour creep rupture strength. As shown in FIG. In 30 to 35, when (Co / W) is 0.75 or more, the creep rupture strength is reduced by 100,000 hours due to the increase, and the decrease is more rapid as the Nb amount is higher. However, when (Co / W) of the material of the present invention is 1.0 or less, the influence of (Co / W) is small, and when (Co / W) is in the range of 0.1 to 0.70, the creep rupture strength. The change in is small.

  FIG. 8 is a diagram showing the relationship between (Co / W) and shock absorption energy. As shown in FIG. 8, when the Nb amount is (Co / W) of 0.75 or more, the shock absorption energy increases as the value increases, but the increase in the shock absorption energy increases more rapidly as the Nb amount increases. . However, when the (Co / W) of the material of the present invention is in the range of 0.1 to 0.70, the change in shock absorption energy is small.

FIG. 9 is a diagram showing the relationship between W / (Mo + 0.5W) and (Co / W). In particular, by adjusting [W / (Mo + 0.5W)] to a range of 1.1 to 1.8 and (Co / W) to a range of 0.1 to 0.90, a temperature of 620 ° C. and a pressure of 25 MPA or more. required 620 ° C. in high pressure and intermediate pressure internal casing and the main steam stop valve and governor valve casing of a high temperature high pressure turbine, 10 ⁵ h creep rupture strength 98MPA above, obtained at room temperature impact absorption energy 29.4J more resistant cast steel casing material It is done.

  FIG. 10 is a diagram showing the relationship between the impact absorption energy on the vertical axis and the creep rupture strength on the horizontal axis. As shown in FIG. 10, the impact absorption energy decreases as the creep rupture strength increases, and has a correlation with the Nb amount described above. Accordingly, No. of the material of the present invention. It is apparent that Nos. 1 to 13 have high impact absorption energy even when compared with a comparative material having the same Nb amount and at the same creep rupture strength.

  FIG. 11 is a diagram showing the relationship between the creep rupture strength on the vertical axis and the impact absorption energy on the blade axis. As shown in FIG. 11, the creep rupture strength decreases as the shock absorption energy increases, and has a correlation with the Nb amount described above. Accordingly, No. of the material of the present invention. It is clear that Nos. 1 to 13 have a high creep rupture strength at the same impact absorption energy even when compared with a comparative material having the same Nb amount.

  FIG. 12 is a front view (a), a side view (b), and a cross-sectional view (c) showing the shape and dimensions of a test piece subjected to a weld crack test on the material of the present invention. The weldability evaluation was performed by an oblique Y-type weld cracking test according to JIS Z3158. Preheating, between passes and after-heat start temperature is 150 ° C., C amount is lowered with respect to the base material, Si amount is about 0.5%, Mn amount is about 1.5%, Ni amount is 0.9%, Mo1 The welding was performed using a coated arc welding rod in which 0.0% was higher than the base metal and other Cr, Nb, V, and N were equivalent to the base metal. The post heat treatment was performed at 400 ° C. for 30 minutes. As shown in Table 2, the inventive material showed no weld cracking and good weldability.

  As described above, according to this embodiment, a ferritic heat-resistant cast steel having a high 620 ° C. creep rupture strength and room temperature toughness can be obtained. Therefore, a casing for an ultra supercritical steam turbine up to a temperature of 650 ° C., a main steam stop valve, steam It can be used for adjusting valves.

  By using the heat-resistant cast steel according to the present invention instead of the austenitic heat-resistant cast steel for the super-supercritical steam turbine casing, main steam stop valve and steam control valve up to 650 ° C, it is manufactured with the same design concept as before. Furthermore, since the coefficient of thermal expansion is smaller than that of austenitic heat-resistant cast steel, there is an advantage that the steam turbine can be started quickly and is not easily damaged by thermal fatigue.

  FIG. 13 is a cross-sectional configuration diagram of a high-pressure steam turbine using the high-strength heat-resistant cast steel of the present invention. FIG. 14 is a cross-sectional configuration diagram of an intermediate pressure steam turbine using the high-strength heat-resistant cast steel of the present invention. The high-pressure steam turbine is provided with a high-pressure rotor shaft 20 in which high-pressure rotor blades 16 are implanted in an inner casing 18 and an outer casing 19 outside the inner casing 18. The intermediate pressure steam turbine is provided with a high pressure rotor shaft 24 in which an intermediate pressure blade 17 is implanted in an inner casing 21 and an outer casing 22 outside the inner casing 21. High-temperature and high-pressure steam is obtained by a boiler, is guided through a main steam pipe, a flange constituting the main steam inlet, the elbow 25, the main steam inlet 28, and the nozzle box 38 to the first stage double-flow rotor blade. A stationary blade is provided for each of these blades.

  In the present embodiment, as a configuration of the steam turbine power plant, a high-pressure steam turbine (HP) and an intermediate-pressure steam turbine (IP) are connected in tandem. The first stage of HP is a double flow, and eight stages are provided on one side. A stationary blade is provided for each of these blades. The moving blade is a saddle type dovetail type and has a double tinon.

  The IP rotates the generator with the HP by the steam heated by the reheater again at 625 ° C. The steam discharged from the HP is rotated at a rotational speed of 3000 times / min. Like the HP, the IP has a medium pressure internal casing 21 and a medium pressure external casing 22, and a stationary blade is provided in opposition to the medium pressure rotor blade 17. The medium pressure rotor blades 17 have two stages and two flows, and are provided on the left and right sides almost symmetrically with respect to the longitudinal direction of the medium pressure rotor shaft 13.

  In this embodiment, both (HP) and (IP) are the outer casings 19 and 22, the inner casings 18 and 21, the main steam stop valve casing and the steam control valve casing described later, as shown in Table 1 of the first embodiment. No. 4 cast steel was used. In particular, 50 tons of an alloy raw material having a target composition for the inner casing was melted in an electric furnace, and after refining a vacuum ladle, it was cast into a sand mold.

The cast steel was annealed at 1050 ° C. × 10 h for furnace cooling, then subjected to normal heat treatment at 1050 ° C. × 10 h for blast cooling, followed by primary tempering at 570 ° C. × 12 h and secondary tempering at 730 ° C. × 12 h. As a result of cutting investigation of this prototype casing having a fully tempered martensite structure, the properties required for a 620 ° C., 25 MPa high temperature and high pressure turbine casing (620 ° C., 10 ⁵ h strength ≧ 98 MPa, room temperature impact absorption energy ≧ 29.4 J) are obtained. While satisfying, it was a thing without a crack in the above-mentioned weld cracking test.

  According to this embodiment, as described above, a ferritic heat-resistant cast steel having a high 620 ° C. creep rupture strength and high room temperature toughness can be obtained. Therefore, it can be used for a casing for an ultra supercritical steam turbine up to a temperature of 650 ° C.

  By using the heat-resistant cast steel according to the present invention instead of the austenitic heat-resistant cast steel for casings for ultra-supercritical steam turbines up to a temperature of 650 ° C., it can be manufactured with the same design philosophy as in the past, and further the austenitic heat-resistant steel. Since the coefficient of thermal expansion is smaller than that of cast steel, there are advantages such that the rapid start-up of the steam turbine is facilitated and that it is less susceptible to thermal fatigue damage.

  Moreover, as a steam turbine power plant of this embodiment, the low-pressure steam turbine (LP) is connected to two tandems and has almost the same structure, and each final stage moving blade has eight stages on the left and right, and is almost symmetrical. In addition, a stationary blade is provided corresponding to the moving blade. The low-pressure rotor shaft is a super-clean tempered bainite of Ni 3.75%, Cr 1.75%, Mo 0.4%, V 0.15%, C 0.25%, Si 0.05%, Mn 0.10%, residual Fe. Forged steel with a texture is used. 12% Cr steel containing 0.1% Mo is used for the moving blades and stationary blades other than the final stage.

  The wing part length of the last stage rotor blade is 43 inches, and the wing part length is 43 inches. The wing part where the high-speed steam of the long blades abuts is provided with a Co-based alloy stellite plate to prevent erosion due to water droplets in the steam. An erosion shield that is joined by welding is provided.

The 43-inch long blade is melted by electroslag remelting and subjected to forging and heat treatment. This long blade material has a weight of C 0.08 to 0.18%, Si 0.25% or less, Mn 0.90% or less, Cr 8.0 to 13.0%, Ni 2 to 3%, Mo 1.5 to 3 From martensitic steel containing 0.0%, V0.05-0.35%, the total amount of one or two of Nb and Ta being 0.02-0.20%, and N0.02-0.10% Thus, the tensile strength at room temperature is 120 kgf / mm ² or more, and it has a fully tempered martensite structure. The mechanical properties of the 43-inch long blade are more preferably a tensile strength of 128.5 kgf / mm ² or more and a 20 ° C. V-notch Charpy impact value of 4 kgf-m / cm ² or more.

  The high-temperature and high-pressure steam turbine power plant in this embodiment is mainly a coal-fired boiler, HP, IP, LP2 units, condenser, condensate pump, low-pressure feed water heater system, deaerator, boost pump, feed water pump, high-pressure feed water It consists of a heater system. That is, the super high temperature and high pressure steam generated in the boiler enters HP and generates power, and then is reheated again in the boiler and enters IP to generate power. The exhaust steam of the IP enters the LP, generates power, and then condenses in the condenser. This condensed water is sent to a low pressure feed water heater system and a deaerator by a condensate pump. The feed water deaerated by the deaerator is sent to a high-pressure feed water heater by a booster pump and a feed pump to be heated, and then returned to the boiler. In the boiler, the feed water becomes high-temperature and high-pressure steam through the economizer, evaporator and superheater.

  Instead of this embodiment, the same HP, IP, and one or two LPs are connected to the tandem, and a tandem compound power plant that generates electricity by rotating one generator can be configured in the same manner. it can.

  According to the present embodiment, it is suitable for a steam turbine casing having a long-term creep rupture strength and toughness necessary under a steam temperature condition of 620 ° C. to 650 ° C., and a steam turbine power plant having high thermal efficiency can be obtained. .

  By using the heat-resistant cast steel according to the present invention instead of the austenitic heat-resistant cast steel for casings for ultra-supercritical steam turbines up to a temperature of 650 ° C., it can be manufactured with the same design philosophy as in the past, and further the austenitic heat-resistant steel. Since the coefficient of thermal expansion is smaller than that of cast steel, there are advantages such that the rapid start-up of the steam turbine is facilitated and that it is less susceptible to thermal fatigue damage.

FIG. 15 is a cross-sectional view of a high-medium pressure integrated steam turbine used in a 600 MW steam turbine power plant with a steam temperature of 620 ° C. This example is a tandem compound double flow type, the last stage blade length in LP is 43 inches, high-medium pressure integrated steam turbine (HP • IP) and LP (1) (C) or 2 (D) 3000 r / min. The high temperature part is composed of the main materials shown in the table. The steam temperature of the high pressure part (HP) is 600 ° C. and a pressure of 250 kgf / cm ² , and the steam temperature of the intermediate pressure part (IP) is heated to 600 ° C. by a reheater, and the pressure is 45 to 65 kgf / cm ² . Driven. Steam having a steam temperature of 400 ° C. enters the low-pressure section (LP) and is sent to the condenser with a vacuum of 100 ° C. or less and 722 mmHg.

  (HP / IP) has a high pressure side steam turbine having an inner casing 18 and an outer casing 19 on the outside thereof, and an intermediate pressure side steam turbine having an inner casing 21 and an outer casing 22 on the outside thereof. A high / medium pressure rotor shaft 23 in which the high pressure blade 16 and the medium pressure blade 17 are implanted is provided. The above-mentioned high-temperature and high-pressure steam is obtained by the above-mentioned boiler, passes through the main steam pipe, passes through the main steam inlet ° C from the flange and elbow 25 constituting the main steam inlet ° C, and passes from the nozzle box 38 to the first stage blade. Led. The rotor blades are provided in 8 stages on the high pressure side on the left side in the figure and 6 stages on the intermediate pressure side (about half of the right side in the figure). A stationary blade is provided for each of these blades. The moving blade has a saddle type or a getter type, a dovetail type, and a double tinon. Further, a main steam stop valve and a steam control valve, which will be described later, are connected to (HP · IP).

  In this example, (HP / IP) outer casings 19 and 22, inner casings 18 and 21, main steam stop valve casings and steam control valve casings described later, No. 1 described in Table 1 of Example 1 were used. In the same manner as in Example 2, using cast steel No. 4, 50 tons of an alloy raw material having a target composition was melted in an electric furnace, refined in a vacuum ladle, cast into a sand mold, and subjected to the same heat treatment.

Also in this example, as a result of investigating this trial casing with a fully tempered martensite structure, characteristics required for a 620 ° C., 25 MPa high temperature and high pressure turbine casing (620 ° C., 10 ⁵ h strength ≧ 98 MPa, room temperature shock absorption) Energy ≧ 29.4 J) and no cracks in the above-described weld cracking test.

  According to this embodiment, as described above, a ferritic heat-resistant cast steel having a high 620 ° C. creep rupture strength and high room temperature toughness can be obtained, so that it can be used for a casing for an ultra supercritical steam turbine up to a temperature of 650 ° C.

  By using the heat-resistant cast steel according to the present invention instead of the austenitic heat-resistant cast steel for casings for ultra-supercritical steam turbines up to a temperature of 650 ° C., it can be manufactured with the same design philosophy as in the past, and further the austenitic heat-resistant steel. Since the coefficient of thermal expansion is smaller than that of cast steel, there are advantages such that the rapid start-up of the steam turbine is facilitated and that it is less susceptible to thermal fatigue damage.

  Further, in the steam turbine power plant of the present embodiment, the low-pressure steam turbine (LP) is connected to one or two tandems and has substantially the same structure as that of the second embodiment, and each final stage moving blade has 8 left and right. There are steps and they are almost symmetrical and can generate 1050 MW power. The blade length of the final stage moving blade is 43 inches, and the same 12% Cr steel as described above is used. The same applies to the low pressure rotor shaft, the moving blades and stationary blades other than the final stage, and the inner and outer casing materials.

  An erosion shield in which a Co-based alloy stellite plate is joined by welding to prevent the erosion caused by water droplets in the steam is provided on the wing part where the wing part has a length of 43 inches.

The 43-inch long blade is melted by electroslag remelting in the same manner as in Example 2 and subjected to forging heat and treatment, and the tensile strength at room temperature is 120 kgf / mm ² or more, more preferably tensile strength. 128.5kgf / mm ² or more, and has a fully tempered martensite structure having a 20 ° C. V-notch Charpy impact value 4kgf-m / cm ² or more.

  According to the present embodiment, it is suitable for a steam turbine casing having long-term creep rupture strength and toughness required under a steam temperature condition of 620 ° C. to 650 ° C., and a steam turbine power plant having high thermal efficiency can be obtained. It is.

  FIG. 16 is a sectional view in which a main steam stop valve and a steam control valve of a steam turbine power plant are integrally formed. In the present embodiment, the main steam sent from the boiler to the high pressure steam turbine or the high / medium pressure integrated steam turbine in the steam turbine power plants of Embodiments 2 and 3 is supplied from the main steam inlet 34 to the main steam stop valve 32, The supply amount is adjusted at the steam outlet 35 by the control valve 33.

  In this example, as the main steam stop valve casing and the steam control valve casing, No. 1 described in Table 1 of Example 1 was used. Using the cast steel of No. 4, the alloy raw material having the target composition was melted in an electric furnace, and after refining the vacuum ladle, it was cast into a sand mold and subjected to the same heat treatment and weld cracking test as in Example 2.

As a result, the properties required for a 620 ° C., 25 MPa high temperature and high pressure turbine casing (620 ° C., 10 ⁵ h strength ≧ 98 MPa, room temperature shock absorption energy ≧ 29.4 J) are satisfied, and there is no crack in the above-mentioned weld crack test. It was a thing.

  According to the present embodiment, as described above, a ferritic heat-resistant cast steel having a high 620 ° C creep rupture strength and high room temperature toughness can be obtained. Therefore, the main steam stop valve casing and steam control of the super supercritical steam turbine up to a temperature of 650 ° C can be obtained. It can be used for a valve casing and has the same effect as described above.

It is a diagram which shows the relationship between W addition amount and 100,000 hours creep rupture strength. It is a diagram which shows the relationship between W addition amount and impact absorption energy. It is a diagram which shows the relationship between Co addition amount and 100,000 hours creep rupture strength. It is a diagram which shows the relationship between Co addition amount and impact absorption energy. It is a diagram which shows the relationship between W / (Mo + 0.5W) and 100,000 hours creep rupture strength. It is a diagram which shows the relationship between the relationship of W / (Mo + 0.5W) and shock absorption energy. It is a figure which shows the relationship between Co / W and 100,000 hours creep rupture strength. It is a diagram which shows the relationship between Co / W and shock absorption energy. It is a diagram which shows the relationship between W / (Mo + 0.5W) and Co / W. It is a diagram which shows the relationship between the impact absorption energy of a vertical axis | shaft, and the creep rupture strength of a horizontal axis | shaft. It is a diagram which shows the relationship between the creep rupture strength of a vertical axis | shaft, and the impact absorption energy of a horizontal axis | shaft. It is a structural diagram of a weld crack test piece. 1 is a cross-sectional structure diagram of a high-pressure steam turbine according to the present invention. It is sectional drawing of the intermediate pressure steam turbine which concerns on this invention. 1 is a cross-sectional view of a high-medium pressure integrated steam turbine according to the present invention. It is sectional drawing of the main steam stop valve and main steam control valve which concern on this invention.

Explanation of symbols

DESCRIPTION OF SYMBOLS 16 ... High pressure moving blade, 17 ... Medium pressure moving blade, 18 ... High pressure inner casing, 19 ... High pressure outer casing, 20 ... High pressure rotor shaft, 21 ... Medium pressure inner casing, 22 ... Medium pressure outer casing, 23 ... High medium pressure one Body rotor shaft, 24 ... medium pressure rotor shaft, 25 ... flange, elbow, 27 ... bearing, 28 ... main steam inlet, 29 ... reheat steam inlet, 30 ... high pressure steam outlet, 31 ... cylinder communication pipe, 32 ... main steam Stop valve, 33 ... Steam control valve, 34 ... Main steam inlet, 35 ... Steam outlet, 38 ... Nozzle box.

Claims (17)

By mass, C0. 10 to 0.16%, Si 0.1 to 0.6 %, Mn 0. 3 ~ 0.8%, Cr 9.5 ~1 1.5%, Ni0.1 2 ~ 0.8%, Mo 0.2~ 0.7%, W1.9~3.0%, V0.05 -0.3%, the total amount of one or more of Nb, Ta and Zr is 0.01-0.15%, Co0. 2 to 1.5 %, N 0.01 to 0.08%, B 0.0005 to 0.010%, Al 0.0005 to 0.04%, O 0.02% or less, the balance being Fe and inevitable impurities A high-strength heat-resistant cast steel characterized by comprising:   The high-strength heat-resistant cast steel according to claim 1, wherein, by mass, Al is 0.0005 to 0.04% and O is 0.02% or less.   The coordinate point A (1.1, 0.90), coordinate point in the orthogonal coordinates represented by the relationship between [W / (Mo + 0.5W)] and (Co / W) according to claim 1 or 2. [W / (Mo + 0.5W)] below each straight line obtained by connecting each point of B (1.5, 0.55) and coordinate point C (1.8, 0.55) with a straight line, and A high-strength heat-resistant cast steel characterized by having (Co / W).   The high-strength heat-resistant cast steel according to any one of claims 1 to 3, characterized by containing at least one of Re 1.5% or less, Nd 0.5% or less, and Sr 1.0% or less by mass. ^{5. The} high-strength heat-resistant cast steel according to claim 1, wherein the creep rupture strength at 620 ° C. for 105 hours is 98 MPa or more and the impact absorption energy at room temperature is 29.4 J or more. By mass, C0. 10 to 0.16%, Si 0.1 to 0.6 %, Mn 0. 3 ~ 0.8%, Cr 9.5 ~1 1.5%, Ni0.1 2 ~ 0.8%, Mo 0.2~ 0.7%, W1.9~3.0%, V0.05 -0.3%, the total amount of one or more of Nb, Ta and Zr is 0.01-0.15%, Co0. A raw material containing 2 to 1.5 %, N 0.01 to 0.08%, B 0.0005 to 0.010%, and the balance consisting of Fe and unavoidable impurities is melted in an electric furnace and vacuum-taken. A method for producing a high-strength heat-resistant cast steel, characterized by casting into a sand mold after degassing by pot refining. By mass, C0. 10 to 0.16%, Si 0.1 to 0.6 %, Mn 0. 3 ~ 0.8%, Cr 9.5 ~1 1.5%, Ni0.1 2 ~ 0.8%, Mo 0.2~ 0.7%, W1.9~3.0%, V0.05 -0.3%, the total amount of one or more of Nb, Ta and Zr is 0.01-0.15%, Co0. 2 ~ 1.5%, N0.01~0.08%, containing B0.0005～0.010%, the cast steel having a composition the balance of Fe and unavoidable impurities, after annealing at 1000 to 1150 ° C. Manufacturing a high-strength heat-resistant cast steel characterized by performing a normalizing heat treatment by heating to 1000 to 1100 ° C. and quenching, followed by primary tempering at 550 to 750 ° C. and secondary tempering at 670 ° C. to 770 ° C. Method.   The method for producing high-strength heat-resistant cast steel according to claim 6 or 7, wherein the mass is Al 0.0005 to 0.04% and O 0.02% or less.   A steam turbine casing comprising the high-strength heat-resistant cast steel according to claim 1.   It manufactures with the manufacturing method of the high strength heat-resistant cast steel in any one of Claims 6-8, The manufacturing method of the steam turbine casing characterized by the above-mentioned.   Steam having a rotor shaft in which a moving blade is implanted, an inner casing that covers a rotor shaft in which a stationary blade corresponding to the moving blade is implanted and in which the moving blade is implanted, and an outer casing that covers the inner casing The steam turbine according to claim 9, wherein the inner casing comprises the steam turbine casing according to claim 9.   A main steam stop valve for controlling supply and stop of main steam obtained by a boiler to a steam turbine, wherein the main steam stop valve casing is made of the high strength heat-resistant cast steel according to any one of claims 1 to 5. A main steam stop valve characterized by   A high-strength heat-resistant cast steel according to any one of claims 6 to 8, wherein the main steam stop valve casing is a main steam stop valve manufacturing method for controlling supply and stop of main steam obtained by a boiler to a steam turbine. A method for manufacturing a main steam stop valve, which is manufactured by the manufacturing method of   In a steam control valve that adjusts the supply amount of the main steam through a main steam stop valve that controls supply and stop of the main steam obtained by the boiler to the steam turbine, the steam control valve casing is defined in claims 1 to 1. A steam control valve comprising the high-strength heat-resistant cast steel according to any one of 5 above.   In a method for manufacturing a steam control valve that adjusts the supply amount of the main steam through a main steam stop valve that controls supply and stop of main steam obtained by the boiler to the steam turbine, the steam control valve casing is claimed. Item 9. A method for producing a steam control valve, which is produced by the method for producing high-strength heat-resistant cast steel according to any one of Items 6 to 8.   A high-pressure steam turbine, an intermediate-pressure steam turbine, and a low-pressure steam turbine coupled to two tandems, or a steam turbine power plant including a high-medium-pressure integrated steam turbine and a low-pressure steam turbine, wherein the high-pressure steam turbine and the intermediate-pressure steam turbine And a steam turbine power plant, wherein at least one of the high and medium pressure integrated steam turbine comprises the steam turbine according to claim 11. A high-pressure steam turbine, a medium-pressure steam turbine, and a low-pressure steam turbine connected to two tandems, or a high-medium-pressure integrated steam turbine and a low-pressure steam turbine, and a boiler for the high-pressure steam turbine or the high-medium-pressure integrated steam turbine in the main steam stop valve and the main steam stop valve steam turbine power plant steam control valve for adjusting the supply amount of which is connected to the main steam through the controlling and stopping the supply of main steam obtained by the At least one of the main steam stop valve and the steam control valve is constituted by the main steam stop valve according to claim 12, and the steam control valve is constituted by the steam control valve according to claim 14. A steam turbine power plant.

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