EP2488672A1 - Homogenization of martensitic stainless steel after remelting under a layer of slag - Google Patents
Homogenization of martensitic stainless steel after remelting under a layer of slagInfo
- Publication number
- EP2488672A1 EP2488672A1 EP10781969A EP10781969A EP2488672A1 EP 2488672 A1 EP2488672 A1 EP 2488672A1 EP 10781969 A EP10781969 A EP 10781969A EP 10781969 A EP10781969 A EP 10781969A EP 2488672 A1 EP2488672 A1 EP 2488672A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- temperature
- ingot
- steel
- homogenization
- slag
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 238000000265 homogenisation Methods 0.000 title claims abstract description 37
- 239000002893 slag Substances 0.000 title claims abstract description 32
- 229910001105 martensitic stainless steel Inorganic materials 0.000 title abstract 2
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 83
- 239000010959 steel Substances 0.000 claims abstract description 83
- 238000001816 cooling Methods 0.000 claims abstract description 37
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 30
- 230000009466 transformation Effects 0.000 claims abstract description 19
- 238000004519 manufacturing process Methods 0.000 claims abstract description 12
- 238000000034 method Methods 0.000 claims description 10
- 229910052799 carbon Inorganic materials 0.000 claims description 6
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 5
- 230000008569 process Effects 0.000 claims description 4
- 238000012423 maintenance Methods 0.000 claims description 3
- 229910001562 pearlite Inorganic materials 0.000 abstract description 2
- 210000001787 dendrite Anatomy 0.000 description 14
- 238000012360 testing method Methods 0.000 description 14
- 239000006185 dispersion Substances 0.000 description 13
- 229910052739 hydrogen Inorganic materials 0.000 description 7
- 230000002028 premature Effects 0.000 description 7
- 238000009661 fatigue test Methods 0.000 description 6
- 238000005204 segregation Methods 0.000 description 6
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 5
- 238000010586 diagram Methods 0.000 description 5
- 238000009792 diffusion process Methods 0.000 description 5
- 239000007792 gaseous phase Substances 0.000 description 5
- 239000001257 hydrogen Substances 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 239000012071 phase Substances 0.000 description 5
- 229910001566 austenite Inorganic materials 0.000 description 4
- 239000007789 gas Substances 0.000 description 4
- 238000000844 transformation Methods 0.000 description 4
- 238000005275 alloying Methods 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- 239000011651 chromium Substances 0.000 description 3
- 125000004122 cyclic group Chemical group 0.000 description 3
- 238000007872 degassing Methods 0.000 description 3
- 230000000977 initiatory effect Effects 0.000 description 3
- 230000009467 reduction Effects 0.000 description 3
- 238000007711 solidification Methods 0.000 description 3
- 230000008023 solidification Effects 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- CPLXHLVBOLITMK-UHFFFAOYSA-N Magnesium oxide Chemical compound [Mg]=O CPLXHLVBOLITMK-UHFFFAOYSA-N 0.000 description 2
- 101150087698 alpha gene Proteins 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 230000003749 cleanliness Effects 0.000 description 2
- 239000012141 concentrate Substances 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 150000001247 metal acetylides Chemical class 0.000 description 2
- 238000010587 phase diagram Methods 0.000 description 2
- 238000010583 slow cooling Methods 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- UDHXJZHVNHGCEC-UHFFFAOYSA-N Chlorophacinone Chemical compound C1=CC(Cl)=CC=C1C(C=1C=CC=CC=1)C(=O)C1C(=O)C2=CC=CC=C2C1=O UDHXJZHVNHGCEC-UHFFFAOYSA-N 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 235000008733 Citrus aurantifolia Nutrition 0.000 description 1
- KRHYYFGTRYWZRS-UHFFFAOYSA-M Fluoride anion Chemical compound [F-] KRHYYFGTRYWZRS-UHFFFAOYSA-M 0.000 description 1
- 235000011941 Tilia x europaea Nutrition 0.000 description 1
- 229910000905 alloy phase Inorganic materials 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 238000013459 approach Methods 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 235000013365 dairy product Nutrition 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000000635 electron micrograph Methods 0.000 description 1
- 230000008030 elimination Effects 0.000 description 1
- 238000003379 elimination reaction Methods 0.000 description 1
- 239000000284 extract Substances 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 230000005251 gamma ray Effects 0.000 description 1
- 229910052500 inorganic mineral Inorganic materials 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 150000002500 ions Chemical class 0.000 description 1
- 239000004571 lime Substances 0.000 description 1
- 239000000395 magnesium oxide Substances 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 239000011707 mineral Substances 0.000 description 1
- 238000009659 non-destructive testing Methods 0.000 description 1
- 230000001902 propagating effect Effects 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 230000000630 rising effect Effects 0.000 description 1
- 238000007493 shaping process Methods 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 239000006228 supernatant Substances 0.000 description 1
Classifications
-
- 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
- C21D6/002—Heat treatment of ferrous alloys containing Cr
-
- 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
- C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
- C22B9/00—General processes of refining or remelting of metals; Apparatus for electroslag or arc remelting of metals
- C22B9/16—Remelting metals
- C22B9/18—Electroslag remelting
Definitions
- the present invention relates to a method for manufacturing a stainless martensitic steel comprising a slag remelting step of an ingot of this steel and a cooling step of this ingot
- a stainless martensitic steel is a steel whose chromium content is greater than 10.5%, and whose structure is essentially martensitic.
- ESR Electro Slag Refusion
- the lower end of this electrode being in contact with the slag, melts and passes through the slag in the form of fine droplets, to solidify below the layer of supernatant slag, into a new ingot that grows gradually.
- the slag acts, inter alia, as a filter which extracts the inclusions from the steel droplets, so that the steel of this new ingot located below the slag layer contains fewer inclusions than the initial ingot (electrode). . This operation is carried out at atmospheric pressure and air.
- Non-destructive ultrasonic testing performed by the inventors, showed that these steels practically had no known hydrogen defects (flakes).
- the dispersion of the fatigue strength results is therefore due to another undesirable mechanism of premature initiation of cracks in the steel, which leads to its premature failure in fatigue.
- the present invention aims to provide a manufacturing method that allows to raise these low values, and thus reduce the dispersion of the fatigue strength of stainless martensitic steels, and also to increase its average value in resistance to fatigue.
- the ingot from the slag remelting is, before the skin temperature of this ingot is less than the martensitic transformation temperature Ms of the steel, placed in an oven whose initial temperature T 0 is then greater than the end of pearlitic transformation temperature in Arl cooling of said steel, this ingot being subjected in this oven to a homogenization treatment for at least one holding time t after the temperature of the coldest point of the ingot has reached a homogenization temperature T, this holding time t being equal to at least one hour, and the homogenization temperature T varying between about 900 ° C and the burn temperature of the steel.
- FIG. 1 compares fatigue life curves for a steel according to the invention and a steel according to the prior art
- FIG. 2 shows a fatigue stress curve
- FIG. 3 is a diagram illustrating dendrites and interdendritic regions
- FIG. 4 is a photograph taken under the electron microscope of a fracture surface after fatigue, showing the gas phase having initiated this fracture.
- FIG. 5 schematically shows cooling curves on a time-temperature diagram for a region richer in alphagenic elements and less rich in gamma-ray elements
- FIG. 6 schematically shows cooling curves on a time-temperature diagram for a region less rich in alpha-gene elements and richer in gammagenic elements.
- the dendrites 10 corresponding to the first solidified grains, are by definition richer in elements.
- alphagenes while the interdendritic regions 20 are richer in gamma-like elements (application of the known rule segments on the phase diagram).
- An alphagene element is one that promotes a ferritic type structure (more stable structures at low temperature, bainite, ferrite-pearlite, martensite).
- a gamma element is an element that promotes an austenitic structure (stable structure at high temperature). There is therefore segregation between dendrites 10 and interdendritic regions 20.
- FIG. 5 is a temperature (T) -time (t) diagram known for a region richer in alphagenes and less rich in gamma elements, such as dendrites 10.
- Curves D and F mark the beginning and the end of the transformation of austenite (region A) into a ferrito-pearlitic structure (FP region). This transformation takes place, partially or fully, when the cooling curve that follows the ingot passes respectively in the region between the D and F curves or in the FP region. It does not occur when the cooling curve is entirely in region A.
- FIG. 6 is an equivalent diagram for a region richer in gammagenic elements and less rich in alphagenic elements, such as the interdendritic regions 20. It will be noted that with respect to FIG. 5, the curves D and F are shifted to the right, that is to say, it will cool more slowly the ingot to obtain a ferritoperlitic structure.
- FIG. 5 and 6 shows three cooling curves from an austenitic temperature, corresponding to three cooling rates; fast (curve C1), average (curve C2), slow (curve C3).
- fast curve C1
- average curve C2
- slow curve C3
- the temperature begins to decrease from an austenitic temperature.
- the cooling rates of the surface and the heart of the ingot are very close. The only difference is that the surface temperature is lower than that of the core because the surface was the first to cool relative to the core.
- the dendrites 10 first turn into ferritic structures during cooling (by crossing the curves D and F of FIG. 5). While the interdendritic regions 20 either do not change (in the case of rapid cooling according to the curve C1) or change later, in whole or in part (in the case of average cooling according to the curve C2 or slow according to the curve C3), to temperatures inferior (see Figure 6).
- the interdendritic regions thus retain a longer austenitic structure.
- the lighter elements are able to diffuse ferritic structure dendrites towards the interdendritic regions 20 of austenitic or all-part structure and to concentrate during the period of coexistence of the ferritic and austenitic structures.
- the risk that the solubility of these light elements is exceeded locally in the interdendritic regions is accentuated. When the concentration in light elements exceeds this solubility, it appears then in the steel microscopic gas pockets containing these light elements.
- the austenite of interdendritic regions tends to locally transform into martensite when the temperature of the steel falls below the martensitic transformation temperature Ms, which is slightly above the temperature. ambient ( Figures 5 and 6).
- martensite has a threshold of solubility in light elements even lower than other metallurgical structures and that austenite. There is therefore more microscopic gaseous phase within the steel during this martensitic transformation.
- This zone P is the imprint of the gaseous phase consisting of the light elements, and which is at the origin of the formation of these fissures F which, by propagating and agglomerating, created a zone of macroscopic fracture.
- the inventors have carried out tests on stainless martensitic steels, and have found that when, immediately after the ESR step, a specific homogenization treatment is carried out on the ingot taken out of the ESR crucible, the formation is reduced. of gaseous phases of light elements.
- the homogenization treatment also leads to a homogenization of the martensitic transformation temperature Ms.
- the diffusion of the alloying elements is far from negligible. Moreover, if the temperature gradient makes it possible to have a warmer surface That the center of the ingot, which the conditions of recovery proposed by the inventors allow, the light elements diffuse towards the surface, which reduces their overall content in the steel.
- the inventors have found that satisfactory results are obtained when the ingot is subjected in this oven to a homogenization treatment during a holding time t after the temperature of the most The cold of this ingot has reached a homogenization temperature T, this time t being equal to at least one hour, and the homogenization temperature T varying between a temperature T min and the burn temperature of this steel.
- the temperature T m j n is approximately equal to 900 ° C.
- the burning temperature of a steel is defined as the temperature in the raw state of solidification at which the grain boundaries in the steel are transformed (or even liquefied), and is greater than T min . This time t of maintaining the steel in the furnace therefore varies inversely with this homogenization temperature T.
- the homogenization temperature T is 950 ° C., and the corresponding holding time t is equal to 70 hours.
- the homogenization temperature T is 1250 ° C. which is slightly lower than the burn temperature, then the corresponding holding time t is equal to 10 hours.
- the homogenization temperature T is selected from a range selected from the group consisting of the following ranges: 950 ° C to 1270 ° C, 980 ° C to 1250 ° C, 1000 ° C to 1200 ° C.
- the minimum hold time t is selected from a range selected from the group consisting of the following ranges: 1 hour to 70 hours, 10 hours to 30 hours, 30 hours to 150 hours.
- the inventors have found that satisfactory results are obtained when the ingot at the outlet of the ESR crucible is placed in an oven whose initial temperature T 0 is greater than the end of pearlitic transformation temperature in cooling Arl of this steel. and when the skin temperature of this ingot remains higher than the martensitic transformation temperature Ms of this steel.
- the initial temperature T 0 of the oven is lower than the homogenization temperature T
- the temperature of the oven is, after the ingot has been placed in this oven, increased to a temperature at least equal to the temperature homogenization.
- the temperature in the center of the ingot therefore remains lower than the skin temperature of the ingot throughout the rise in temperature. This allows a global degassing and more effective ingot.
- the initial temperature T 0 of the oven may be greater than the homogenization temperature, in which case the oven temperature is simply maintained above this homogenization temperature.
- the inventors have found that the homogenization treatment is especially necessary when:
- the maximum dimension of the ingot is less than approximately 910 mm, and the H content of the ingot before slag remelting is greater than 10 ppm, and
- the maximum dimension of the ingot is greater than about 910 mm and the minimum dimension of the ingot is less than about 1500 mm, and the H content of the ingot before slag remelting is greater than 3 ppm, and
- the minimum dimension of the ingot is greater than 1500 mm and the H content of the ingot before slag remelting is greater than 10
- the maximum dimension of the ingot is that of the measurements in its most massive part, and the minimum dimension of the ingot is that of the measures in its least massive part;
- the concentrations of light elements may be greater (greater than 10 ppm) when the minimum dimension of the ingot or of the deformed ingot is greater than a large size threshold (in this case 1500 mm).
- a high threshold (1500 mm) for the minimum dimension of the ingot is as follows: when the minimum dimension of the ingot is greater than this threshold, we approach the case of slow cooling (curve C3) in which there is almost no structural difference between dendrites and interdendritic regions during cooling.
- the cooling rate is sufficiently low so that the temperature is substantially homogeneous between the core of the skin of the ingot, so that the diffusion of light elements to the surface is facilitated, which allows a greater degassing.
- the core of the ingot is, during the cooling, much hotter than its surface, which favors a diffusion of the light elements towards the core and slows down the degassing.
- the slag is previously dehydrated before use in the ESR crucible, because it minimizes the amount of hydrogen present in the slag, and thus minimizes the amount of hydrogen that could pass the slag ingot during the ESR process.
- the inventors have carried out tests on Z12CNDV12 steels produced with the process according to the invention, that is to say with a homogenization carried out immediately after the ingress of the ingot of the ESR crucible according to the following parameters:
- Test No. 1 skin temperature of the ingot at 250 ° C., put in the oven at 400 ° C., rise of the oven at the homogenization temperature of 1250 ° C., metallurgical maintenance (as soon as the coldest temperature of the ingot reaches the homogenization temperature) of 75h, cooling to room temperature.
- Test No. 2 Skin temperature of the ingot at 600 ° C., put in the oven at 450 ° C., rise of the furnace at the homogenization temperature of 1000% metallurgical maintenance (as soon as the coldest temperature of the ingot reaches the temperature homogenization) of 120h, cooling to room temperature. The results of these tests are presented below,
- composition of the Z12CNDV12 steels is the following (standard DMD0242-20 index E):
- the martensitic transformation temperature Ms measured is 220 ° C.
- the amount of Hydrogen measured on the ingots before slag remelting varies from 3.5 to 8.5 ppm.
- Figure 1 qualitatively shows the improvements made by the method according to the invention.
- the value of the number N of rupture cycles necessary to break a steel specimen subjected to a cyclic stress in tension as a function of the pseudo-alternating stress C is obtained experimentally (this is the stress experienced by the test specimen under imposed deformation. , according to Sncma DMC0401 standard used for these tests).
- Such a cyclic bias is shown schematically in FIG. 2.
- the period T represents a cycle.
- the constraint evolves between a maximum value C ma x and a minimum value C min .
- the first curve 15 (in fine lines) is (schematically) the average curve obtained for a steel produced according to the prior art.
- This first average curve CN is surrounded by two curves 16 and 14 in dashed fine lines. These curves 16 and 14 are situated respectively at a distance of +3 ⁇ s ⁇ and -3 at t from the first curve 15, where ⁇ * is the standard deviation of the distribution of the experimental points obtained during these fatigue tests. and ⁇ 3 ⁇ statistically corresponds to a confidence interval of 99.7%.
- the distance between these two curves 14 and 16 in dashed line is therefore a measure of the dispersion of results.
- Curve 14 is the limiting factor for dimensioning a part.
- the second curve 25 (in thick line) is (schematically) the average curve obtained from the results of fatigue tests carried out on a steel produced according to the invention under a load according to FIG. CN average curve is surrounded by two curves 26 and 24 dashed thick line, respectively located at a distance of +3 ⁇ 2 and -3 ⁇ 2 of the second curve 25, ⁇ 2 being the standard deviation of the distribution of points experimental results obtained during these fatigue tests.
- Curve 24 is the limiting factor for dimensioning a part.
- the second curve 25 is located above the first curve 15, which means that under fatigue stress at a stress level C, the steel test pieces produced according to the invention break on average to a number N of cycles higher than that where the steel test pieces according to the prior art are broken.
- the distance between the two curves 26 and 24 in thick dashed line is smaller than the distance between the two curves 16 and 14 in dashed fine lines, which means that the dispersion in fatigue resistance of the developed steel according to the invention is lower than that of a steel according to the prior art.
- Oligocyclic fatigue means that the bias frequency is of the order of 1 Hz (the frequency being defined as the number of periods T per second).
- the minimum value of fatigue stress required to break a steel according to the invention is greater than the minimum fatigue stress value M (set at 100%) necessary to break a steel according to the prior art.
- the carbon content of the stainless martensitic steel is lower than the carbon content below which the steel is hypoeutectoid, for example a content of 0.49%.
- a low carbon content allows a better diffusion of the alloying elements and a lowering of the temperatures of solution of the primary or noble carbides, which leads to a better homogenization.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Physics & Mathematics (AREA)
- Manufacturing & Machinery (AREA)
- Manufacture And Refinement Of Metals (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
- Treatment Of Steel In Its Molten State (AREA)
Abstract
Description
Claims
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
FR0957108A FR2951197B1 (en) | 2009-10-12 | 2009-10-12 | HOMOGENIZATION OF STAINLESS STEEL MARTENSITIC STEELS AFTER REFUSION UNDER DAIRY |
PCT/FR2010/052140 WO2011045513A1 (en) | 2009-10-12 | 2010-10-11 | Homogenization of martensitic stainless steel after remelting under a layer of slag |
Publications (2)
Publication Number | Publication Date |
---|---|
EP2488672A1 true EP2488672A1 (en) | 2012-08-22 |
EP2488672B1 EP2488672B1 (en) | 2019-05-08 |
Family
ID=41728409
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP10781969.0A Active EP2488672B1 (en) | 2009-10-12 | 2010-10-11 | Homogenization of martensitic stainless steel after remelting under a layer of slag |
Country Status (9)
Country | Link |
---|---|
US (1) | US8911527B2 (en) |
EP (1) | EP2488672B1 (en) |
JP (1) | JP5868859B2 (en) |
CN (1) | CN102575313B (en) |
BR (1) | BR112012008520B1 (en) |
CA (1) | CA2777034C (en) |
FR (1) | FR2951197B1 (en) |
RU (1) | RU2536574C2 (en) |
WO (1) | WO2011045513A1 (en) |
Families Citing this family (2)
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US9601857B2 (en) | 2013-05-23 | 2017-03-21 | Pulse Electronics, Inc. | Methods and apparatus for terminating wire wound electronic devices |
US9716344B2 (en) | 2013-07-02 | 2017-07-25 | Pulse Electronics, Inc. | Apparatus for terminating wire wound electronic components to an insert header assembly |
Family Cites Families (22)
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GB1361046A (en) * | 1970-07-10 | 1974-07-24 | Arbed | Additives for melting under an electro conductive slag |
AT331434B (en) * | 1974-05-28 | 1976-08-25 | Ver Edelstahlwerke Ag | PROCEDURE FOR REMOVING UNWANTED ELEMENTS, IN PARTICULAR H2 AND O2 DURING ELECTRIC SLAG REMOVAL AND ARRANGEMENT FOR CARRYING OUT THE PROCEDURE |
JPS52120208A (en) * | 1976-04-02 | 1977-10-08 | Nippon Kokan Kk <Nkk> | Heating of homogenizing furnace |
JPS52143907A (en) * | 1976-05-25 | 1977-11-30 | Sumitomo Metal Ind Ltd | Arr angement of upper end burner in continuous heating furnace |
SU1014934A1 (en) * | 1980-01-02 | 1983-04-30 | Предприятие П/Я Р-6209 | Method for heat treating stainless steel |
SU1142517A1 (en) * | 1983-08-18 | 1985-02-28 | Предприятие П/Я М-5729 | Method of heat treatment of stainless and maraging steel castings |
US4832909A (en) * | 1986-12-22 | 1989-05-23 | Carpenter Technology Corporation | Low cobalt-containing maraging steel with improved toughness |
JPH0673686B2 (en) | 1989-10-06 | 1994-09-21 | 住友金属工業株式会社 | Rolling method for martensitic stainless steel |
US5524019A (en) * | 1992-06-11 | 1996-06-04 | The Japan Steel Works, Ltd. | Electrode for electroslag remelting and process of producing alloy using the same |
JP2781325B2 (en) | 1993-06-17 | 1998-07-30 | 川崎製鉄株式会社 | Method for producing medium and high carbon martensitic stainless steel strip having fine carbides |
JPH08100223A (en) | 1994-10-03 | 1996-04-16 | Hitachi Metals Ltd | Production of high cleanliness steel |
US6273973B1 (en) | 1999-12-02 | 2001-08-14 | Ati Properties, Inc. | Steelmaking process |
AU2003241253C1 (en) * | 2002-06-13 | 2009-05-14 | Uddeholms Ab | Cold work steel and cold work tool |
DE60331111D1 (en) * | 2002-11-19 | 2010-03-11 | Hitachi Metals Ltd | Process for producing martensitic hardening steel |
EP1689902A4 (en) * | 2003-11-12 | 2007-08-22 | Questek Innovations Llc | Ultratough high-strength weldable plate steel |
WO2006081401A2 (en) * | 2005-01-25 | 2006-08-03 | Questek Innovations Llc | MARTENSITIC STAINLESS STEEL STRENGTHENED BY NI3TI η-PHASE PRECIPITATION |
US8071017B2 (en) * | 2008-02-06 | 2011-12-06 | Fedchun Vladimir A | Low cost high strength martensitic stainless steel |
FR2935623B1 (en) | 2008-09-05 | 2011-12-09 | Snecma | METHOD FOR MANUFACTURING CIRCULAR REVOLUTION THERMOMECHANICAL PIECE COMPRISING STEEL-COATED OR SUPERALLIATION TITANIUM-BASED CARRIER SUBSTRATE, TITANIUM-FIRE RESISTANT TURBOMACHINE COMPRESSOR CASE |
FR2935625B1 (en) | 2008-09-05 | 2011-09-09 | Snecma | METHOD FOR MANUFACTURING A CIRCULAR REVOLUTION THERMAMECHANICAL PART COMPRISING A STEEL-COATED OR SUPERALLIATION TITANIUM-BASED CARRIER SUBSTRATE, TITANIUM-FIRE RESISTANT TURBOMACHINE COMPRESSOR CASE |
FR2935624B1 (en) | 2008-09-05 | 2011-06-10 | Snecma | METHOD FOR MANUFACTURING CIRCULAR REVOLUTION THERMOMECHANICAL PIECE COMPRISING STEEL-COATED OR SUPERALLIATION TITANIUM-BASED CARRIER SUBSTRATE, TITANIUM-FIRE RESISTANT TURBOMACHINE COMPRESSOR CASE |
US8557059B2 (en) * | 2009-06-05 | 2013-10-15 | Edro Specialty Steels, Inc. | Plastic injection mold of low carbon martensitic stainless steel |
FR2947566B1 (en) | 2009-07-03 | 2011-12-16 | Snecma | PROCESS FOR PRODUCING A MARTENSITIC STEEL WITH MIXED CURING |
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2009
- 2009-10-12 FR FR0957108A patent/FR2951197B1/en active Active
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2010
- 2010-10-11 WO PCT/FR2010/052140 patent/WO2011045513A1/en active Application Filing
- 2010-10-11 US US13/501,377 patent/US8911527B2/en active Active
- 2010-10-11 CA CA2777034A patent/CA2777034C/en active Active
- 2010-10-11 BR BR112012008520-4A patent/BR112012008520B1/en active IP Right Grant
- 2010-10-11 CN CN201080046202.XA patent/CN102575313B/en active Active
- 2010-10-11 JP JP2012533671A patent/JP5868859B2/en active Active
- 2010-10-11 RU RU2012119594/02A patent/RU2536574C2/en active
- 2010-10-11 EP EP10781969.0A patent/EP2488672B1/en active Active
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Also Published As
Publication number | Publication date |
---|---|
RU2012119594A (en) | 2013-11-20 |
JP2013507530A (en) | 2013-03-04 |
CA2777034C (en) | 2017-11-07 |
FR2951197A1 (en) | 2011-04-15 |
BR112012008520B1 (en) | 2018-04-17 |
CN102575313A (en) | 2012-07-11 |
WO2011045513A1 (en) | 2011-04-21 |
US8911527B2 (en) | 2014-12-16 |
CN102575313B (en) | 2015-11-25 |
EP2488672B1 (en) | 2019-05-08 |
RU2536574C2 (en) | 2014-12-27 |
FR2951197B1 (en) | 2011-11-25 |
JP5868859B2 (en) | 2016-02-24 |
CA2777034A1 (en) | 2011-04-21 |
US20120260771A1 (en) | 2012-10-18 |
BR112012008520A2 (en) | 2016-04-05 |
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