US3917493A - Austenitic heat resisting steel - Google Patents
Austenitic heat resisting steel Download PDFInfo
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- US3917493A US3917493A US387736A US38773673A US3917493A US 3917493 A US3917493 A US 3917493A US 387736 A US387736 A US 387736A US 38773673 A US38773673 A US 38773673A US 3917493 A US3917493 A US 3917493A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
Definitions
- JlS Japanese Industrial Standards
- SUS- 29 and SUS-43 steel (AISl-32l and 347 steel as similar standards) among l8Cr-8Ni austenitic stainless steels are generally employed for elevated temperature and high pressure services.
- the feature of SUS-29 steel (AlSl-32l steel) lies in that Ti is added in connection with C content and that og SUS-43 steel (AlSI-347 steel), Nb is added in the same manner.
- These steels aimed at high temperature strength of more than 600C.
- SUS-27 steel A181- 304 steel
- This invention has been developed in order to meet 2 perature than those of ordinary stainless steels in the JIS, e.g. SUS-29 (AlSl-32l) or SUS-43 (AlSI-347).
- Another object of this invention is to provide a heat resisting steel having excellent heat resistance for long period of time at elevated temperature, which is based on synergestic effect depending upon the coexisting of (Nb+Zr) or (Nb+Zr+Ti).
- Figure is a diagram showing creep rupture strength of this invention steels arranged with the atomic ratio of (Nb+Zr+Ti)/C.
- This invention steel has the following composition; that is,
- the reason for simultaneously adding said. additional elements i.e. coexistance of (Nb+Zr) or (Nb-l-ZH-Ti) in steel, lies in that the coexistance of these elements are effective for preventing formed carbides from coalescing and for causing said carbides to disperse uniformly. With this, the strength at an elevated temperature and for a long period of time service is improved remarkably.
- the fact that single addition of Nb, Zr, or Ti is very insufficient to improve said strength is made clear in many experiments based on the prior art. Therefore, the simultaneous addition as mentioned above, i.e. coexistance of these elements in steel, becomes an indispensable requirement of this invention. Such details will be apparent from the following examples.
- Chemical composition of tested steels is as follows.
- Nb and Zr are simultaneously These steels are hot-rolled to the thickness of 12 mm added in the range of which the atomic ratio of (Nb+Zr)/C is 0.05 to 1.0.
- Ti are further added to the above composition in the range which the atomic ratio of (Nb+Zr+Ti)/C is 0.05 to 1.0.
- An object of this invention is to provide an economical heat resisting steel having higher strength and better heat resistance for long period of time at elevated temand then are subjected to solution treatment of being heated-up to 1,100C and soaked at the same temperature for 1 hr, then water-quenched.
- the results of creep rupture test by ordinary test pieces cut off from the above-mentioned plates are shown in Table II and the changes of said creep rupture strength at 650C X0 10 hr. depending upon said atomic ratio is shown in the accompanying drawing.
- said strength of a usual stainless steel, i.e. steel A is too low for a long period of time services at an elevated temperature.
- said strength of the single-added steel of Nb, Zr, or Ti i.e. steel D, E and F, is little improved for said services.
- the coexisting steels of (Nb+Zr), i.e. steel Bl B3, and of (Nb+Zr+Ti), i.e. C1 C3 exhibit superior strength in comparison with other steels, i.e. steels A,
- Such a range is selected from the scope that the atomic ratio of (Nb+Zr) or (Nb+Zr+Ti) to C, wherein C is 0.03 to 0.30% and Nb, Zr or Ti is 0.02 to 1.0% respectively, is from 0.05 to 1.0, preferably 0.2 to 0.5 as shown in the drawing.
- C content of this invention is selected from 0.03 to 0.3%. Actually, it should be decided in connection with the later-mentioned atomic ratio. In such a case, Cr carbide is possible to be made to precipitate and disperse around Nb and Zr or Nb, Zr and Ti carbides with out any coalescence bringing about the lowering of said strength. This behavior results in improvement of said heat resistance for a long period of time service at an elevated temperature.
- Nb, Zr or Ti These elements are added in steel with Zr wt% Zr atomic wt Nb wt% b atomic wt
- said atomic ratio must be adjusted within the range of 0.05 to 1.0, preferably 0.2 to 0.5.
- said content of C, Nb and Zr should be selected from the abovementioned range to obtain the required atomic ratio. It is needless to say that said atomic ratio of (Nb+Zr+Ti) to C is also calculated with the same manner.
- the atomic ratio also may be substitued with the weight ratio of (Nb+Zr) or (Nb+Zr+Ti) to C. in such a case, said weight ratio is calculated with the fol-, lowing formula and becomes frow 0.4 to 8.0 in correspondence with said atomic ratio of 0.05 to 1.0.
- said atomic ratio of 0.05 to 1.0 is equal to said weight ratio of 0.4 to 8.0.
- a steel plate having the above-mentioned composition is prepared by hot or cold working after usual steel making.
- the obtained plate should be heated up to 1050C or more and soaked for at least 10 min, then is water-quenched.
- carbides and nitrides of Nb, Zr and Ti are solution-treated into matrix of said steel, simultaneously, the grain size is adjusted to N 0.4 to 0.8 of ASTM.
- a method of making austenitic heat resistant steel comprising:
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- Mechanical Engineering (AREA)
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- Heat Treatment Of Steel (AREA)
Abstract
An austenitic heat resisting steel exhibiting excellent strength for a long period of time services at an elevated temperature, coexistant-adding 0.02 to 1.0% Nb and 0.02 to 1.9% Zr or 0.02 to 1.0% Nb, 0.02 to 1.0% Zr and 0.02 to 1.0% Ti in addition to usual composition of a stainless steel, simultaneously adjusting the atomic ratio of said (Nb+Zr) or (Nb+Zr+Ti) to C within the range of 0.05 to 1.0, preferably 0.2 to 0.5.
Description
Mimino et a1.
atet [1 1 [4 1 Nov. 4, 1975 AUSTENITIC HEAT RESISTING STEEL Inventors: Tohru Mimino, Tokyo; Kazuhisa Kinoshita, Yokohama; Takayuki Shinoda, Tokyo; lsao Minegishi,
Yokohama, all of Japan Nippon Kokan Kabushiki Kaisha, Tokyo, Japan Filed: Aug. 13, 1973 Appl. No.: 387,736
Assignee:
US. Cl. 148/12 E; 75/128 0; 75/128 2;
, 75/128 T int. c1. (3211) 7/14; c22c 38/48; c22c 38/50 Field of Search 148/12 E, 12.3; 75/128 0 References Cited UNITED STATES PATENTS 3/1952 Payson 75/128 G 4 Creep Rupture Streng1h1650C lO hr) 5 U1 2,823,114 2/1958 Eberle 75/128 G 2,957,790 10/1960 Metcalfe 148/123 3,669,759 6/1972 Kondo et a1. 148/123 3,795,509 3/1974 Mimino et a1. 75/128 G 3,826,689 7/1974 Ohta et a1. 148/12 E Primary Examiner-W. Stallard Attorney, Agent, or Firm-William Anthony Drucker 57 1 ABSTRACT An austenitic heat resisting steel exhibiting excellent strength for a long period of time services at an elevated temperature, coexistant-zadding 0.02 to 1.0% Nb and 0.02 to 1.9% Zr or 0.02 to 1.0% Nb, 0.02 to 1.0% Zr and 0.02 to 1.0% Ti in addition to usual composition of a stainless steel, simultaneously adjusting the atomic ratio of said (Nb+Zr) or (Nb+Zr+Ti) to C within the range of 0.05 to 1.0, preferably 0.2 to 0.5.
4 Claims, 1 Drawing Figure AUSTENITIC HEAT RESISTING STEEL This invention relates to composition of improving heat resistance of austenitic heat resisting steel, and more particularly, strength for a long period time ser vices at an elevated temperature.
It is well known that higher strength and better oxidation resistance of steel for long period of time at elevated temperature are required in some services such as tubings for boiler, chemical facilities and atomic power. For example, as the boiler becomes large-sized and ultracritical pressure typed, higher strength of employed steels has been called for said services.
At present, JlS (Japanese Industrial Standards) SUS- 29 and SUS-43 steel (AISl-32l and 347 steel as similar standards) among l8Cr-8Ni austenitic stainless steels are generally employed for elevated temperature and high pressure services. In the above case, the feature of SUS-29 steel (AlSl-32l steel) lies in that Ti is added in connection with C content and that og SUS-43 steel (AlSI-347 steel), Nb is added in the same manner. These steels aimed at high temperature strength of more than 600C. However, according to many experiments, it is evidently confirmed that said strength of the above steels is inferior to that of SUS-27 steel (A181- 304 steel) not containing Ti or Nb. That is, it is discovered that creep rupture strength of SUS-29 and 43 steel falls rapidly as servicing temperature becomes higher and employing time becomes longer. For example, said strength of SUS-27 steel at 700 C X 10 hr. is 4.3 Kg/mm while both SUS-29 and 43 steel are 4 Kg/mm in the same manner. It is presumed that this deterioration of said strength is due to that Ti and Nb carbide coalesces and precipitates in grain boundary during servicing for long period of time at higher temperature.
Thus, a heat resisting steel being inex-pensive and having higher strength is not yet provided for industrial circles. It is a fact that development of some economical heat resisting steels is required today.
This invention has been developed in order to meet 2 perature than those of ordinary stainless steels in the JIS, e.g. SUS-29 (AlSl-32l) or SUS-43 (AlSI-347).
Another object of this invention is to provide a heat resisting steel having excellent heat resistance for long period of time at elevated temperature, which is based on synergestic effect depending upon the coexisting of (Nb+Zr) or (Nb+Zr+Ti).
Additional object of this invention will become apparent by the following description refering to the examples and the accompanying drawings, in which:
Figure is a diagram showing creep rupture strength of this invention steels arranged with the atomic ratio of (Nb+Zr+Ti)/C.
This invention steel has the following composition; that is,
C: 0.03 to 0.30% by weight Si: up to 1.0% by weight Mn: up to 2.00% by weight Cr: 15.0 to 26.0% by weight Ni: 7.0 to 22.0% by weight the atomic ratio of (Nb+Zr)/C or (Nb+Zr+Ti)/C is from 0.05 to 1.0% respectively at the range of which Nb, Zr or Ti is from 0.02 to 1.0% respectively, unavoidable impurities and the balance being Fe.
As mentioned above, the reason for simultaneously adding said. additional elements, i.e. coexistance of (Nb+Zr) or (Nb-l-ZH-Ti) in steel, lies in that the coexistance of these elements are effective for preventing formed carbides from coalescing and for causing said carbides to disperse uniformly. With this, the strength at an elevated temperature and for a long period of time service is improved remarkably. The fact that single addition of Nb, Zr, or Ti is very insufficient to improve said strength is made clear in many experiments based on the prior art. Therefore, the simultaneous addition as mentioned above, i.e. coexistance of these elements in steel, becomes an indispensable requirement of this invention. Such details will be apparent from the following examples.
Chemical composition of tested steels is as follows.
TABLE Chemical composition of tested steel (weight 70) (Nb+Ze+Ti)/c Steel C Si Mn Cr Ni Nb Zr Ti atomic ratio A 0.17 0.54 1.58 18.32 10.15 B1 0.16 0.55 1.57 18.09 10.10 0.090 0.066 0.12 B2 0.15 0.57 1.56 17.89 9.92 0.191 0.238 0.38 B3 0.16 0.59 1.51 17.95 9.98 0.655 0.606 1.03 Cl 0.16 0.56 1.60 18.04 10.01 0.097 0.027 0.047 0.17 oz 0.17 0.55 1.55 17.81 9.92 0.308 0.114 0 089 0.45 C3 0.16 0.55 1.54 18.25 9.83 0.601 0.202 0.181 0.94 B4 0.15 0.58 1.55 17.80 10.11 0.99 0.98 171 C4 015 0.57 1.45 18.02 9.89 1.01 0.32 0.30 1.65 D 0.15 0.51 1.59 17.65 9.58 0.29 0.48 E 0.14 0.55 1.41 18.20 9.86 0.25 0.24 F 0.15 0.53 1.58 17.54 10.10 0.33 0.28
the above requirements. One of the features of this invention lies in that both Nb and Zr are simultaneously These steels are hot-rolled to the thickness of 12 mm added in the range of which the atomic ratio of (Nb+Zr)/C is 0.05 to 1.0. Another feature of this invention lies in that Ti are further added to the above composition in the range which the atomic ratio of (Nb+Zr+Ti)/C is 0.05 to 1.0.
An object of this invention is to provide an economical heat resisting steel having higher strength and better heat resistance for long period of time at elevated temand then are subjected to solution treatment of being heated-up to 1,100C and soaked at the same temperature for 1 hr, then water-quenched. The results of creep rupture test by ordinary test pieces cut off from the above-mentioned plates are shown in Table II and the changes of said creep rupture strength at 650C X0 10 hr. depending upon said atomic ratio is shown in the accompanying drawing.
TABLE 11 Creep rupture strength of tested steels Kg/mm 650C 700C Steel l' hr l0hr l0'-hr l0hr A 15.0 11.2 9.7 7.1 B1 18.5 14.5 1 1.4 8.6 B2 19.0 14.7 11.7 9.0 B3 16.8 12.7 10.9 8.0 Cl 18.0 14.0 12.4 9.2 C2 18.0 14.1 12.2 92 C3 17.4 13.2 10.5 8.2 B4 15.1 11.5 9.9 7.3 C4 15.5 11.7 10.2 7.6 D 15.3 1 1.6 9.5 7.0 E 16.2 12.3 10.3 7.5 F 6.5 12.4 10.5 7.4
Atomic Ratio= N These steels are grouped together with a usual stainless steel-(steel A), coexisting steels of (Nlrl-Zfl-(steel B1 B4), coexisting steels of (Nb+Zr+Ti)-(steel C1 C4) and single-added steels of Nb, Zr or Ti (steel D, E and F). According to the above Tables 1 and 11, it will be well understood that the change of said neat resistance for a long period of time services at an elevated temperature depends upon the composition, specially, how the selected elements, i.e. Nb, Zr or Ti, are added and what the atomic ratio of the said elements to carbon is. That is, first, said strength of a usual stainless steel, i.e. steel A is too low for a long period of time services at an elevated temperature. Secondly, said strength of the single-added steel of Nb, Zr, or Ti, i.e. steel D, E and F, is little improved for said services. Thirdly, the coexisting steels of (Nb+Zr), i.e. steel Bl B3, and of (Nb+Zr+Ti), i.e. C1 C3, exhibit superior strength in comparison with other steels, i.e. steels A,
, D, E and F. Fourthly, said strength of steels in which said atomic ratio of (Nb+Zr) or (Nb+Zr+Ti) to C exceeds 1.0, i.e. steel B4 and C4, are as low as that of steels A, D, E and F, evenif (Nb+Zr) or (Nb-l-Ti) is coexistently added. It is understood from the above results that the coexisting condition of (Nb+Zr) or (Nb+Zr+Ti) in steel should be adjusted to the most suitable range. Such a range is selected from the scope that the atomic ratio of (Nb+Zr) or (Nb+Zr+Ti) to C, wherein C is 0.03 to 0.30% and Nb, Zr or Ti is 0.02 to 1.0% respectively, is from 0.05 to 1.0, preferably 0.2 to 0.5 as shown in the drawing.
The reason why the most suitable range is set up in the present invention is as follows.
C: C content of this invention is selected from 0.03 to 0.3%. Actually, it should be decided in connection with the later-mentioned atomic ratio. In such a case, Cr carbide is possible to be made to precipitate and disperse around Nb and Zr or Nb, Zr and Ti carbides with out any coalescence bringing about the lowering of said strength. This behavior results in improvement of said heat resistance for a long period of time service at an elevated temperature.
Cr: less than 15.0% Cr brings about a change of oxinection with the above Cr content.
4 Si: and Mn: These elements are enough to be in the usual range of stainless steel.
Nb, Zr or Ti: These elements are added in steel with Zr wt% Zr atomic wt Nb wt% b atomic wt When weight and atomic weight of eachof C, Nb and Zr are substituted in the above formula, the required atomic ratio can be easily obtained. In the present invention, said atomic ratio must be adjusted within the range of 0.05 to 1.0, preferably 0.2 to 0.5. In other words, said content of C, Nb and Zr should be selected from the abovementioned range to obtain the required atomic ratio. It is needless to say that said atomic ratio of (Nb+Zr+Ti) to C is also calculated with the same manner. The atomic ratio also may be substitued with the weight ratio of (Nb+Zr) or (Nb+Zr+Ti) to C. in such a case, said weight ratio is calculated with the fol-, lowing formula and becomes frow 0.4 to 8.0 in correspondence with said atomic ratio of 0.05 to 1.0.
Weight Rat|o= C wt% 0.4 8.0
That is, said atomic ratio of 0.05 to 1.0 is equal to said weight ratio of 0.4 to 8.0.
A steel plate having the above-mentioned composition is prepared by hot or cold working after usual steel making. The obtained plate should be heated up to 1050C or more and soaked for at least 10 min, then is water-quenched. With the above process, carbides and nitrides of Nb, Zr and Ti are solution-treated into matrix of said steel, simultaneously, the grain size is adjusted to N 0.4 to 0.8 of ASTM.
Thus, when a steel is prepared as mentioned above and interrelation among C, Nb, Zr and Ti is adjusted to the scope of said atomic ratio or said weight ratio, excellent heat resistance for a long period of time at an elevated temperature can be obtained with stability and ease.
We claim:
1. A method of making austenitic heat resistant steel comprising:
forming a steel mixture of iron and the following ingredients in weight percent proportions:
C-0.03 to 0.30%; Si0 to 1.00%; Mn-O to 2.00%;
Cr-l5.0 to 26.0%; Ni-7.0 to 22%; and each of Nb,Zr,Ti0.02 to 1.0%; wherein the Nb,Zr,Ti atomic ratio to C is within the range of 0.05 to 1.0; working the mixture into a plate; heat treating the plate above 1050C for at least 10 minutes; and thereafter water quenching the steel.
2. A method of making austentic heat resistant steel compnsmg:
6 plate above l050C for at least 10 minutes; and thereafter water quenching the steel. 3. A method according to claim 1 in which the working includes hot working into a plate.
4. A method according to claim 1 in which the method includes cold working into a plate.
Claims (4)
1. A METHOD OF MAKING AUSTENTIC HEAT RESISTANT STEEL COMPRISING: FORMING A STEEL MIXTURE OF IRON AND THE FOLLOWING INGREDIENTS, IN WEIGHT PERCENT PROPORTIONS: C-0.03 TO 0.30%, SI-0 TO 1.00, MN-0 TO 2.00%, CR15.0 TO 26.0%, NI-7.0 TO 22%, AND EACH OF NB,ZR,TI-0.02 TO 1.0%, WHEREIN THE NB,ZR,TI ATOMIC RATIO TO C IS WITHIN THE RANGE OF 0.05 TO 1.0, WORKING THE MIXTURE INTO A PLATE, HEAT TREATING THE PLATE ABOVE 1050*C FOR AT LEAST 10 MINUTES, AND THEREAFTER WATER QUENCHING THE STEEL.
2. A method of making austentic heat resistant steel comprising: forming a steel mixture of iron and the following ingredients in weight percent proportions: C-0.03 to 0.30%; Si-0 to 1.00%; Mn-0 to 2.00%; Cr-15.0 to 26.0%; Ni-7.0 to 22%; Nb-0.02 to 1%; and Zr-0.02 to 1.9%; wherein the Nb,Zr atomic ratio to C is within the range of 0.2 to 0.5; working the mixture into a plate; heat treating the plate above 1050*C for at least 10 minutes; and thereafter water quenching the steel.
3. A method according to claim 1 in which the working includes hot working into a plate.
4. A method according to claim 1 in which the method includes cold working into a plate.
Priority Applications (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US387736A US3917493A (en) | 1973-08-13 | 1973-08-13 | Austenitic heat resisting steel |
| US05/553,945 US3940267A (en) | 1973-08-13 | 1975-02-28 | Austenitic heat resisting steel |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US387736A US3917493A (en) | 1973-08-13 | 1973-08-13 | Austenitic heat resisting steel |
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| Application Number | Title | Priority Date | Filing Date |
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| US05/553,945 Division US3940267A (en) | 1973-08-13 | 1975-02-28 | Austenitic heat resisting steel |
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| Publication Number | Publication Date |
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| US3917493A true US3917493A (en) | 1975-11-04 |
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| US387736A Expired - Lifetime US3917493A (en) | 1973-08-13 | 1973-08-13 | Austenitic heat resisting steel |
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4119456A (en) * | 1977-01-31 | 1978-10-10 | Steel Founders' Society Of America | High-strength cast heat-resistant alloy |
| US4360390A (en) * | 1979-09-06 | 1982-11-23 | Nippon Steel Corporation | Method for direct heat treating austenitic stainless steel wire rod |
| FR2790089A1 (en) * | 1999-02-23 | 2000-08-25 | Commissariat Energie Atomique | Monitoring and prediction of physical, mechanical or chemical properties of a metal alloy, namely austenitic stainless steel used as nuclear reactor core material, involves determining the total mass fraction precipitated in the alloy |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2587613A (en) * | 1948-12-02 | 1952-03-04 | Crucible Steel Company | High temperature high strength alloys |
| US2823114A (en) * | 1954-07-30 | 1958-02-11 | Babcock & Wilcox Co | Forgeable high strength austenitic alloy with columbium-tantalum addition |
| US2957790A (en) * | 1960-03-16 | 1960-10-25 | Universal Cyclops Steel Corp | Method of making cold worked and aged products which are substantially free of objectionable lamellar constituent from precipitation hardenable ferrous base alloys |
| US3669759A (en) * | 1968-09-27 | 1972-06-13 | Japan Atomic Energy Res Inst | Thermomechanical treatment for improving ductility of carbide-stabilized austenite stainless steel |
| US3795509A (en) * | 1967-11-10 | 1974-03-05 | Nippon Kokan Kk | Austenitic steel of the cr-ni-mn group |
| US3826689A (en) * | 1971-03-09 | 1974-07-30 | Kobe Steel Ltd | Austenite type heat-resisting steel having high strength at an elevated temperature and the process for producing same |
-
1973
- 1973-08-13 US US387736A patent/US3917493A/en not_active Expired - Lifetime
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2587613A (en) * | 1948-12-02 | 1952-03-04 | Crucible Steel Company | High temperature high strength alloys |
| US2823114A (en) * | 1954-07-30 | 1958-02-11 | Babcock & Wilcox Co | Forgeable high strength austenitic alloy with columbium-tantalum addition |
| US2957790A (en) * | 1960-03-16 | 1960-10-25 | Universal Cyclops Steel Corp | Method of making cold worked and aged products which are substantially free of objectionable lamellar constituent from precipitation hardenable ferrous base alloys |
| US3795509A (en) * | 1967-11-10 | 1974-03-05 | Nippon Kokan Kk | Austenitic steel of the cr-ni-mn group |
| US3669759A (en) * | 1968-09-27 | 1972-06-13 | Japan Atomic Energy Res Inst | Thermomechanical treatment for improving ductility of carbide-stabilized austenite stainless steel |
| US3826689A (en) * | 1971-03-09 | 1974-07-30 | Kobe Steel Ltd | Austenite type heat-resisting steel having high strength at an elevated temperature and the process for producing same |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4119456A (en) * | 1977-01-31 | 1978-10-10 | Steel Founders' Society Of America | High-strength cast heat-resistant alloy |
| US4360390A (en) * | 1979-09-06 | 1982-11-23 | Nippon Steel Corporation | Method for direct heat treating austenitic stainless steel wire rod |
| FR2790089A1 (en) * | 1999-02-23 | 2000-08-25 | Commissariat Energie Atomique | Monitoring and prediction of physical, mechanical or chemical properties of a metal alloy, namely austenitic stainless steel used as nuclear reactor core material, involves determining the total mass fraction precipitated in the alloy |
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