US3440038A - High tenacity chromium-nickel manganese austenitic steel - Google Patents
High tenacity chromium-nickel manganese austenitic steel Download PDFInfo
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- US3440038A US3440038A US521275A US3440038DA US3440038A US 3440038 A US3440038 A US 3440038A US 521275 A US521275 A US 521275A US 3440038D A US3440038D A US 3440038DA US 3440038 A US3440038 A US 3440038A
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- Prior art keywords
- steel
- high tenacity
- alloy
- chromium
- heat
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- 229910000831 Steel Inorganic materials 0.000 title description 34
- 239000010959 steel Substances 0.000 title description 34
- WHROWQPBDAJSKH-UHFFFAOYSA-N [Mn].[Ni].[Cr] Chemical compound [Mn].[Ni].[Cr] WHROWQPBDAJSKH-UHFFFAOYSA-N 0.000 title description 3
- 229910045601 alloy Inorganic materials 0.000 description 27
- 239000000956 alloy Substances 0.000 description 27
- 239000011572 manganese Substances 0.000 description 16
- 239000011651 chromium Substances 0.000 description 10
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 9
- 229910052799 carbon Inorganic materials 0.000 description 6
- 229910052804 chromium Inorganic materials 0.000 description 6
- 229910052748 manganese Inorganic materials 0.000 description 6
- 229910052710 silicon Inorganic materials 0.000 description 6
- 229910052717 sulfur Inorganic materials 0.000 description 5
- 230000007797 corrosion Effects 0.000 description 4
- 238000005260 corrosion Methods 0.000 description 4
- 150000001247 metal acetylides Chemical class 0.000 description 4
- 229910052759 nickel Inorganic materials 0.000 description 4
- 229910052698 phosphorus Inorganic materials 0.000 description 4
- 229910052721 tungsten Inorganic materials 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 3
- 230000003647 oxidation Effects 0.000 description 3
- 238000007254 oxidation reaction Methods 0.000 description 3
- 238000003466 welding Methods 0.000 description 3
- 229910000851 Alloy steel Inorganic materials 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- 229910052796 boron Inorganic materials 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 229910052750 molybdenum Inorganic materials 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- -1 CrS Chemical class 0.000 description 1
- 229910001347 Stellite Inorganic materials 0.000 description 1
- 235000013524 arak Nutrition 0.000 description 1
- 235000020053 arrack Nutrition 0.000 description 1
- 230000003190 augmentative effect Effects 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- AHICWQREWHDHHF-UHFFFAOYSA-N chromium;cobalt;iron;manganese;methane;molybdenum;nickel;silicon;tungsten Chemical compound C.[Si].[Cr].[Mn].[Fe].[Co].[Ni].[Mo].[W] AHICWQREWHDHHF-UHFFFAOYSA-N 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000001627 detrimental effect Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000003779 heat-resistant material Substances 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 238000005121 nitriding Methods 0.000 description 1
- 230000001473 noxious effect Effects 0.000 description 1
- 238000007747 plating Methods 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- WWNBZGLDODTKEM-UHFFFAOYSA-N sulfanylidenenickel Chemical compound [Ni]=S WWNBZGLDODTKEM-UHFFFAOYSA-N 0.000 description 1
- 150000004763 sulfides Chemical class 0.000 description 1
- 238000004381 surface treatment Methods 0.000 description 1
- 229910052715 tantalum Inorganic materials 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Images
Classifications
-
- 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
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F02—COMBUSTION ENGINES; HOT-GAS OR COMBUSTION-PRODUCT ENGINE PLANTS
- F02B—INTERNAL-COMBUSTION PISTON ENGINES; COMBUSTION ENGINES IN GENERAL
- F02B3/00—Engines characterised by air compression and subsequent fuel addition
- F02B3/06—Engines characterised by air compression and subsequent fuel addition with compression ignition
Description
A ril 22, 1969 YOSHIRO ARAKI & 9
HIGH TENACITY CHROMIUM-NICKEL MANGANESE AUSTENITIC STEEL Filed Jan. 18, 1966 United States Patett O 3,440,038 HIGH TENACITY CHROMIUM-NICKEL MANGANESE AUSTENITIC STEEL Yosliro Arak, Tokyo, Japan, assignor to Mitsubishi Jukogyo Kabushiki Kaisha, Tokyo, Japan Filed Jan. 18, 1966, Ser. No. 521,275 Claims priority, application Japan, Feb. 6, 1965, 40/6,503 Int. CI. C22c 41/02, 39/26, 39/44 U.S. Cl. 75-128 4 Claims ABSTRACT OF THE DISCLOSURE This invention relates to new and improved high tenacity austenitic steels.
The heat-resistant steels of the prior art, to be employed for exhaust valves of internal combuston engines, for turbine blades and for the like are generally decient in at least one respect. Among the shortcomngs of the heat-resistant sfeels of the prior art are the following: extreme lowering'of the mechanical properties at high temperatures, especially at temperatures of about 750 C.; poor processability, especially machinability, forgeability and weldability; only a few of these steels are both very highly oxidation-resistant at high temperatures and very highly corrosion-resistant to -P bO; the steels possessing a convenient hardness have poor tenacity and low elongation; and poor fatigue resistance at high temperatures. Furthermore, previous solutions of the foregoing shortcomings have been highly uneconomical. A major object of this invention is to provide a highly economical, high tenacity austenitic steel of general utility, which is 'also heat-resistant, and which has none of the shortcomings referred to above.
In the description of the invention which follows and in the claims, all proportions are given by weight based on the total weight of the steel and all elements and compounds are referred to by their common chemical abbreviation (such as Mn for manganese, Ni for nickel, Cr for chromium, NiS for nickel sulfide, etc.) rather than by their full name. Since the steels of the present invention are alloys they will frequently herein so be referred to.
FIGS. 1 and 2 each show an engine valve incorporating alloy of the present invention;
FI'GS. 3 and 4 each show a precombusticn `chamber mouth piece of a diesel engine incorporating alloy of the present invention;
'FIG. S shows a turbine rotor made of an alloy of the present invention, mounted on a shaft;
FIG. 6 shows a turbocharger bl-ade made of an alloy of the present invention, mounted on a shaft.
Accord-ing to the present invention, Mn is found to be desirable to elevate the stability of the austenite and simultaneously to increase the solid solubility of other elements added. By incorporating Mn in an amount not higher than 6.4% the formation of carbide is aided and the tenacity and heat-rollabil-ity of the product are improved. Ni is found to be desirable in an amount of 6.1%-l1.l%, as by the presence thereof jointly with Mn the favo-rable effects of the Mn are augmented and 3,440,038 Patented Apr. 22, 1969 F V CC the strength at both high and lo w temperatures is substantially improved. Because of the presence of the Ni, the amount of Mn used is less than 11.9%.
Cr forms double carbides. However, it is found desirable to incorporate only l6.0-2'2.0% Cr, which is sufficient for the attainment of good oxidation resistance.
W forms the M C, =M C series of carbides, where the metallic (M) portion includes Fe.Cr.W or Fe.Cr.W.Mo or the like, when the steel is heat treated. 'It is found desirable to incorporate an amount of W of up to 2.l%.
It is found that N and 'C together increase the hardness and strength of the steel and that the presence of Mn elevates the solid solubility of the N. It is found that suitable amounts of N are 0.09 to 059% and of C are '0.31 to 057%.
As Si greatly increases the acid-resistance at high temperatures, the add-tion of a small amount thereof is found to be desirable; however, because it has the tendency to subs*antially reduce the strength of the steel -at high temperatures and, generally, when the amount of Si is great, the resistance to Pb'O corrosion, which re sistance is necessary for a valve steel, is greatly lowered, in the alloy of this invention it is found that a suitable amount of 'S-i is low, only 0.11-1.91%, so that the resistance to PbO corrosion is not reduced.
B greatly improves the hardenability of the steel. In the alloy of this invention, it is found desirable to use more B than in common heat resistant steel; however, it is also found desi'rable that the amount of B should not be so great as to cause excessive hardness and brittleness upon heat treatment of the steel. Accordingly, the amount -of B found des-ira'ble is 0.005`l-0.'22%. Good carbide formation also results.
The in'corporation of 0.01-0.12% -S is found to give good machinability to the alloys of this invention after the beat-treatment, and by the presence of Mn the formation of noxious sul fides, such as CrS, FeS, Nis and the like, is prevented and innoxious Mn'S is stably produced.
Mo, with W, is found to efficiently form fine carbides; but, as it is found to have a tendency to greatly reduce the acid-resistance of the steel at temperatures above 800 C., less than 12% -of Mo is used.
Below 045% total of Nb and/or Ta may be used ac cording to the present invention because they promote the stabilization of the carbides and regulation of the crystal grains.
By the addition of a small amount of other elements according to the invention, namely, of Ti, Al, Cu and V, the hardening of the steel may be improved and, as Al also increases the oxidation-resistance, the addition of less than 3% total of these elements is advantageous.
In order to best coordinate the efect of the added elements, it is found that the following relations should obtain: Mn+Ni=1'2.0-19.0% and The balance of the steel of the present invention is Fe.
By a convenient heat-treating of the alloy of this invention excellent tenacity 'and processability thereof are obtained. The beat-treatment constitutes heating the alloy to a 'temperature of 1020-11 C. and holding it at this elevated temperature for about one hour and thereafter cooling it, for example with water, to 700-780* C. and holding it at that temperature for 4-24 hours.
'In the drawings 1 indicates steel of this invention and 2, 2', 2, 2'", and 2'' indicate heat-resistant steels of the prior art.
'FIGURE 1 shows an engine valve joined by resistance welding to a valve body made of an alloy of this invention 1 with a valve rod made of a prior art heat-resistant steel 2, such as SEH 3 or the like. SEH 3 is the Japanese 3 code for a steel which is 0.35-0.45% C., 1.80-2.50% Si, no more than about 06% Mn, 10-1`3% Cr, 0.70- 1.30% Mo, no more than about 003% P, no more than about 0.03% S and the balance Fe.
FIGURlES 3 and 4 show a precombustion ohamber mouth piece of a disesel engine made by resistance welding a mouth piece composed of alloy of this invention to a base seat of low alloy steel such as S 45C, SCM 3 or the like and by adjoining the other parts therewith.
FIGURE 5 shows a turbine rotor made of the alloy of this invention with a shaft of low alloy steel such as S 45C, SCM 3 or the li ke. FIGURE 6 is a turbocharger blade obtained by fixing a blade made of the al'loy of this invention to a shaft of S 45C, SCM 3 or the like. The alloy of the present invention is useful for all types of service, such as for use as a nonmagnetie material or as a heat-resistant material. S 4-5C and SCM 3 are Japanese codes for steels. S 45C is 0.50-0.60% C, 0.l5-0.40% Si, 0.40-080% Mn, no more than 0.45 P, no more than 0.45 S and the balance Fe. SCM 3 is 0.33-0.3-8% C, 0.1S-0.3*5% Si, 0.'60-0.85% Mn, 0.90 to 1.20% Cr, `0.15-0.35% Mo, no more than 4 SEH 4 is the Japanese code for an austenitic beat-rcsistant steel which is 0.35-0.45% C, l.50-2.50% Si, no more about 0.6% Mn, 13.0-`l5.0% Ni, 14.0-16.0% Cr, 2.0-3.0% W, no more than 003% P, no more than about 0.03% S and the balance Fe.
In perfect austenitic steel, fissures are easily originated at high temperatures by the production of CrS; but in the alloys of the present invention, even if the amount of S is increased, CrS is not produced, that is, although they are not ferrite, the alloys of this invention a'c fissure-resistant. Furthermore, the alloys of this invention contain no sigma phase, the presence of which would be detrimental. They also possess good mechinability due to the presence of MnS instead of CrS.
The alloys of this invention possess good processability in all respects and the machinability thereof is so good that they are able to be turned at the rate of 160 m./rnin. Also, their weldability is good and friction welding thereof is possible. Furthermore, surface-treatment thereof, such as metal plating, nitriding, cementation and the like, is easy, and they are excellent also in their ability to be heat-rolled.
The compositions and properties of seven specific alloys according to this invention (a to g) are set forth separately in Tables 1 and 2 respectively. In Table 1, the proportions of elements are by weight percentage of the total and the unlisted balance to make 100% is Fe.
TAB LE 1 C Si M Ni Cr W N S B TAB LE 2 Tensile st'eng th, Impact value, Oxidation PbO weight Creep rupture kg./mm. Elongation, kgm./cm. Hardness weight increase, decrease, strength, percent, 20 C. 20 C. (Re), 20 C. gr./m 900 C./ gr./dm. /h. kgJmrnfl, 20 C 800 C 100 h. 920 C. 700 C./1,000 h.
003% P, no more than about 003% S and the balance Fe.
Alloys of the present invention, heat-treated as described above, have a tensile strength of about 99i4 kgJrnm. at room temperature, a tensile strength of about 4023 kg./mm. at 800 C., an impact value of above 4 kgm./cm. and an elongation of above 25%, and can be -stretched at room temperature.
The carbide formed by the beat-treatment, having M C as a core, is very stable; the properties thereof undergo essentially no change even if it is heated up to 750 C. for 1000 hours.
Alloys of the present invention are perhaps lower in 'hardness than heat-resistant Valve steels of the prior art; however, the strength and hardness of the alloys of this invention decrease little at high temperatures and they have outstanding abrasion-resistance.
Alloys of this invention undergo only a small increase of oxidatior in the atmosphere at 800 C. as Compared With room temperature; thus, for example, this increase is only one-half that which the austenitic heat-resistant valve steel disclosed in U.S. Patent No. 2,657,130 undergoes. Also, the alloys of this invention undergo only a very small loss by corrosion into mol-ten PbO at 1000 C.; for example, the loss is as small as one-twentieth that of SEH 4 heat-resistant steel. Furthermore, in the alloys of this invention, although the oXidation-resistance is notably elevated by the presence of Si, the lowering of corrosion-resistance to PbO caused thereby is very small.
The invention is not to be construed as limited to the particular forms described herein, since these are to be regarded as illustrative rather than restrictive.
What I claim and desire to secure by Letters Patent is:
1. A high tenacity austenitic steel consistng essentially of 0.31 to 057% C, 0.11 .to 1.9l% Si, 6.4-11.9% Mn, 6.1 to 11.1% Ni, 16.0 to 220% Cr, 0.40 to 2.l0% W, 0.09 to 059% N, 0.0051 to 022% B, 0.01 to 0.12% S, and Fe, the total of Mn and Ni being 12.0 to 19% and the total of C, Si, W, N, S and B being 1.4 to 4.2%.
2. A high tenacity austenitic steel according to claim 1, further containing Mo in an amount no` greater than 12%.
3. A high tenacity austenitic steel according to claim 1, further containing at least one of Nb and Ta, in a total amount no greater than 0.45
4. A high tenacity austenitic steel according to claim 1, further containing at least one of Ti, Al, Cu and V in a total amount no greater than 3%.
References Cited UNITED STATES PATENTS 2,602,738 7/1952 Jennings. 2,80l,9l6 8/1957 Harris 75-128.4 3,3 06,736 2/1967 Rundell.
HYLAND BIZOT, Primary Exam'ner.
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP650365 | 1965-02-06 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| US3440038A true US3440038A (en) | 1969-04-22 |
Family
ID=11640225
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| US521275A Expired - Lifetime US3440038A (en) | 1965-02-06 | 1966-01-18 | High tenacity chromium-nickel manganese austenitic steel |
Country Status (2)
| Country | Link |
|---|---|
| US (1) | US3440038A (en) |
| GB (1) | GB1077592A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4842782A (en) * | 1986-10-14 | 1989-06-27 | Allergan, Inc. | Manufacture of ophthalmic lenses by excimer laser |
| EP0467756A1 (en) * | 1990-07-18 | 1992-01-22 | AUBERT & DUVAL | Austenitic steel having improved strength properties at high temperature, process for its manufacturing and the fabrication of mechanical parts, more particularly of valves |
| US20050132695A1 (en) * | 2003-12-17 | 2005-06-23 | Ingersoll-Rand Energy Systems Corporation | Single-piece turbine rotor and pinion gear and manufacturing technique for same |
| CN104213044A (en) * | 2014-08-26 | 2014-12-17 | 清华大学 | Copper alloy die-casting die steel and manufacturing method thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2602738A (en) * | 1950-01-30 | 1952-07-08 | Armco Steel Corp | High-temperature steel |
| US2801916A (en) * | 1954-08-24 | 1957-08-06 | Jessop William & Sons Ltd | Ferrous alloys for high temperature use |
| US3306736A (en) * | 1963-08-30 | 1967-02-28 | Crucible Steel Co America | Austenitic stainless steel |
-
1966
- 1966-01-18 US US521275A patent/US3440038A/en not_active Expired - Lifetime
- 1966-01-31 GB GB4109/66A patent/GB1077592A/en not_active Expired
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2602738A (en) * | 1950-01-30 | 1952-07-08 | Armco Steel Corp | High-temperature steel |
| US2801916A (en) * | 1954-08-24 | 1957-08-06 | Jessop William & Sons Ltd | Ferrous alloys for high temperature use |
| US3306736A (en) * | 1963-08-30 | 1967-02-28 | Crucible Steel Co America | Austenitic stainless steel |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4842782A (en) * | 1986-10-14 | 1989-06-27 | Allergan, Inc. | Manufacture of ophthalmic lenses by excimer laser |
| EP0467756A1 (en) * | 1990-07-18 | 1992-01-22 | AUBERT & DUVAL | Austenitic steel having improved strength properties at high temperature, process for its manufacturing and the fabrication of mechanical parts, more particularly of valves |
| FR2664909A1 (en) * | 1990-07-18 | 1992-01-24 | Aubert & Duval Acieries | AUSTENITIC STEEL HAVING IMPROVED RESISTANCE AT HIGH TEMPERATURE AND PROCESS FOR OBTAINING SAME AND PRODUCING MECHANICAL PARTS, ESPECIALLY VALVES. |
| US20050132695A1 (en) * | 2003-12-17 | 2005-06-23 | Ingersoll-Rand Energy Systems Corporation | Single-piece turbine rotor and pinion gear and manufacturing technique for same |
| US7089728B2 (en) * | 2003-12-17 | 2006-08-15 | Ingersoll-Rand Energy Systems Corporation | Single-piece turbine rotor and pinion gear and manufacturing technique for same |
| CN104213044A (en) * | 2014-08-26 | 2014-12-17 | 清华大学 | Copper alloy die-casting die steel and manufacturing method thereof |
| CN104213044B (en) * | 2014-08-26 | 2016-04-06 | 清华大学 | One Albatra metal-die-casting die steel and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| GB1077592A (en) | 1967-08-02 |
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