EP3617333A1 - Procédé de fabrication d'un produit d'acier hypereutectoïde par traitement thermomécanique - Google Patents
Procédé de fabrication d'un produit d'acier hypereutectoïde par traitement thermomécanique Download PDFInfo
- Publication number
- EP3617333A1 EP3617333A1 EP19193739.0A EP19193739A EP3617333A1 EP 3617333 A1 EP3617333 A1 EP 3617333A1 EP 19193739 A EP19193739 A EP 19193739A EP 3617333 A1 EP3617333 A1 EP 3617333A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- blank
- point
- product
- working
- cycles
- 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.)
- Withdrawn
Links
- 238000000034 method Methods 0.000 title claims abstract description 34
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 26
- 239000010959 steel Substances 0.000 title claims abstract description 26
- 230000000930 thermomechanical effect Effects 0.000 title claims abstract description 8
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 6
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 18
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 17
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 16
- 238000001816 cooling Methods 0.000 claims abstract description 10
- 239000002994 raw material Substances 0.000 claims abstract description 10
- 229910052742 iron Inorganic materials 0.000 claims abstract description 9
- 239000000654 additive Substances 0.000 claims abstract description 7
- 150000003839 salts Chemical class 0.000 claims abstract description 5
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 5
- 238000010791 quenching Methods 0.000 claims description 14
- 230000000171 quenching effect Effects 0.000 claims description 14
- 238000010438 heat treatment Methods 0.000 claims description 10
- 150000001247 metal acetylides Chemical class 0.000 claims description 8
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 6
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims description 6
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims description 6
- 239000005864 Sulphur Substances 0.000 claims description 6
- 229910052698 phosphorus Inorganic materials 0.000 claims description 6
- 239000011574 phosphorus Substances 0.000 claims description 6
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 4
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 3
- 229910052750 molybdenum Inorganic materials 0.000 claims description 3
- 239000011733 molybdenum Substances 0.000 claims description 3
- 229910052759 nickel Inorganic materials 0.000 claims description 3
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims description 3
- 229910052720 vanadium Inorganic materials 0.000 claims description 3
- 230000000712 assembly Effects 0.000 claims description 2
- 238000000429 assembly Methods 0.000 claims description 2
- 239000012535 impurity Substances 0.000 claims description 2
- 239000008188 pellet Substances 0.000 claims description 2
- 239000003923 scrap metal Substances 0.000 claims description 2
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims 2
- 238000006243 chemical reaction Methods 0.000 claims 1
- 230000003716 rejuvenation Effects 0.000 claims 1
- 239000000956 alloy Substances 0.000 abstract description 8
- 229910045601 alloy Inorganic materials 0.000 abstract description 4
- 229910000975 Carbon steel Inorganic materials 0.000 description 6
- 238000010606 normalization Methods 0.000 description 6
- 230000002411 adverse Effects 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 3
- 238000005520 cutting process Methods 0.000 description 3
- 229910000734 martensite Inorganic materials 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 238000005496 tempering Methods 0.000 description 2
- ODAOZWTYNWZSBY-SPIKMXEPSA-N (z)-but-2-enedioic acid;6-[2-(1h-imidazol-5-yl)ethylamino]-n-[4-(trifluoromethyl)phenyl]heptanamide Chemical compound OC(=O)\C=C/C(O)=O.OC(=O)\C=C/C(O)=O.C=1N=CNC=1CCNC(C)CCCCC(=O)NC1=CC=C(C(F)(F)F)C=C1 ODAOZWTYNWZSBY-SPIKMXEPSA-N 0.000 description 1
- 229910001208 Crucible steel Inorganic materials 0.000 description 1
- 229910000677 High-carbon steel Inorganic materials 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- 239000004411 aluminium Substances 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 239000011203 carbon fibre reinforced carbon Substances 0.000 description 1
- 239000010962 carbon steel Substances 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- -1 chrome carbides Chemical class 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000010924 continuous production Methods 0.000 description 1
- 230000001627 detrimental effect Effects 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 239000011572 manganese Substances 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 239000003921 oil Substances 0.000 description 1
- 231100000614 poison Toxicity 0.000 description 1
- 230000007096 poisonous effect Effects 0.000 description 1
- 238000003672 processing method Methods 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- GPPXJZIENCGNKB-UHFFFAOYSA-N vanadium Chemical compound [V]#[V] GPPXJZIENCGNKB-UHFFFAOYSA-N 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
Images
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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/32—Soft annealing, e.g. spheroidising
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/78—Combined heat-treatments not provided for above
- C21D1/785—Thermocycling
-
- 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
- C21D5/00—Heat treatments of cast-iron
-
- 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
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
-
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
Definitions
- the object of the invention is a method for manufacturing a low-alloy hypereutectoid steel product by thermomechanical processing, in which
- High-carbon steels are currently invariably used with a carbon content of up to approximately 2.0 %. With high carbon concentrations, a considerable hardness is imparted to the steel, but at the expense of brittleness.
- Such steel is also very durable as a result of the action of the carbides therein, but nevertheless so brittle that its potential uses are quite limited. Typical uses are, inter alia, pulling tools, cutting blades, that are not subjected to impact stresses or high temperatures, and razor blades.
- the cast steel products require "normalization” in order to remove the coarse cast structure. Normalization is further used to eliminate inhomogeneities in forged objects as well as phenomena ( inter alia grain growth) caused by an uneven heating of welded or flame-cut products. By means of normalization, the structure can again be rendered “fine-grained” and its mechanical properties simultaneously restored.
- the steel is heated to an austenitic phase and is kept there until the "austenite” is homogenized and subsequently air-cooled.
- a resilient and finely distributed "ferritic-perlitic" microstructure is achieved with the non-alloy structure steels.
- the object of the invention is to provide a pure, in particular additive-free high-carbon steel product that has good strength properties.
- the characterizing features of the invention are indicated in the claims.
- the correct temperature of austenization annealing is important for normalization, as it is for other thermal processes. If austenization occurs at a temperature that is too high, grain growth is the consequence. For this reason, the austenization temperature with normal carbon steels can only be above an approximately 50 °C A 3 point.
- a steel processing method similar to this invention is disclosed in the inventor certificate SU 456841 , but it only applies to a carbon content of over 2 %. The document also does not disclose any information beyond the processing of the blank.
- thermomechanical processing the closest to the initial processing in accordance with the invention is an HTMT process in which a blank with a carbon content of 0.5% is subjected to high-temperature thermomechanical processing.
- U.S. patent no. 3459599 discloses a method for thermomechanically quenching and tempering steel. In this process, the steel is worked vigorously slightly above the A 1 temperature and finally slightly below the latter. The steel contains chrome and manganese.
- the patent US3178324 of the same applicant discloses a hypereutectoid, multi-cycle quenching and tempering always down to room temperature, but without working. In order to attain a fine-grained steel without alloy materials, the object is heated and cooled drastically above the A 1 point, so that the structure changes repeatedly between the martensitic and austenitic states while a heating to a temperature that accelerates grain growth is avoided. The cooling phase each time is rapid so that the change in state occurs in the ferritic direction.
- Expensive alloy materials can be avoided - with inexpensive materials unique results are achieved. Alloy materials react in different ways to heat and some are poisonous. A product in accordance with the invention is natural and thus easy to recycle.
- excess carbon is collected into evenly dispersed small carbide pockets. This is achieved by means of a rapid cooling and a small amount of sulphur and/or phosphorus, which form carbide nuclei in the absence of "better” additives.
- the evenly dispersed small carbide pockets participate during the series of cycles in working as well as in the A 1 lattice transformation.
- the method in accordance with the invention requires a remarkable level of expertise.
- the hot working of the blank for attaining the product occurs within a narrow temperature range - heating momentarily and precisely to approximately 800 °C. Heating does not reach an austenitic phase (point A cm ), but the A 1 point is crossed. In the series of cycles, during working, the cooling is not particularly rapid so that the structure does not become heavily martensitic at any given time.
- the weldability of the product obtained with the method according to the invention is outstanding and a welding rod can be made from the same.
- the cutting ability of the product is outstanding (the cutting blade keeps its sharpness - shiny finish).
- the thickness of the product to be quenched is advantageously 2 - 20 mm, most advantageously 5 - 12 mm.
- the weight of the object can also vary significantly, typically 50 g - 30 kg, as the thinnest dimension is the most significant.
- a continuous process is also possible, e.g. a process for a 400 - 1200 mm steel band requires several consecutive furnace-correction-roller assemblies, after which there is a quenching unit, from which the product is either wound onto a large drum or cut into sheets.
- FIG. 2 shows a sectional view of a steel product in accordance with the invention. The grain boundaries are not visible to the naked eye.
- This steel is, apart from its high carbon content, by composition a conventional fine-grained steel. Alloy materials are not at all necessary, as the processes in accordance with the invention impart a fine granularity, strength and hardness. The most important aspect for its properties is the combined multi-stage thermal and working processing or thermomechanical processing.
- the fine-grained and evenly dispersed carbides break up the lattice cells during the series of cycles, from which the freed atoms move to the grain boundaries and plug them.
- the success of the final result can be checked by checking whether or not the grain boundaries are visible to the naked eye.
- the cooled object is in an austenitic + cementite phase and the nuclei of the hypereutectoid carbides are produced in this case either inside the crystals or at the grain boundaries under the influence of the working.
- the formation of adverse carbide networks at the grain boundaries is substantially reduced for this reason while working is continued.
- Carbides are formed more evenly both inside the crystals and at the grain boundaries.
- the carbon content is 0.8-2.0 % depending on the desired properties.
- the sulphur and phosphorus content must be kept low, but a small quantity of the same is required for the formation of the carbide nuclei.
- thermomechanical processing means that there is nothing else in the blank besides iron and carbon.
- concentrations of additives in the raw material are very low.
- the sulphur content is nevertheless 0.007 - 0.038% and/or the phosphorus content is in the range of 0.005 - 0.026 %, so that the carbides with the most advantageous nuclei are formed. Aluminium and silicon are detrimental in this regard. Their concentrations must be extremely slight.
- a raw material is chosen or produced that is free of vanadium, wolfram, molybdenum, chrome and nickel, the raw material, however, thus containing small quantities of sulphur and/or phosphorus for forming the carbide nuclei. It is possible to select a pure scrap metal while avoiding adverse additives that cannot be removed by means of refining processes.
- composition of raw ore is known and does not contain any adverse compounds.
- an ideal raw material is obtained. Any hydrogen in the raw ore must be removed. It causes hydrogen occlusions.
- carbon in a concentration of 0.8 - 2.0 %, most advantageously 1.6 - 1.9 %, is added to the molten iron.
- the blank is cast and cooled rapidly, a 5 kg object with salt water or at a corresponding speed, whereupon the mentioned carbide nuclei are formed so as to be small in size and evenly dispersed.
- Casting is carried out at a rather low temperature, at 1500 °C. It is left to cool rapidly, as it is not possible to exploit the heat of the cast.
- the speed of cooling can be fixed to be the same as that of a chill cast of a 5kg pellet with a cross section of 50 mm x 100 mm, ⁇ 30%. If the blank does not turn out, it must be heated again to over 1140 °C, generally in the range of 1000 - 1220 °C and the process started again from the beginning.
- the blank is worked into its final shape.
- the temperature is above the A 1 point, but is below the A 1 point right at the end in order to preserve its properties.
- the blank is quenched into its final shape by heating it to approximately 780 °C, after which it is immediately rapidly quenched, blank having a cross section of 5 mm x 100 mm by salt water, ⁇ 30%, or by a method producing a corresponding cooling speed.
- the quenched blank can be tempered in a known manner.
- a thin object can also be quenched with oil. How the quenching is realized depends on the intended use and the composition of the object. If quenching is performed at the end, the final result is clearly martensitic. If less quenching is performed, the final result is bainitic or contains residual austenite. Quenching can optionally be performed as a surface quenching with quenching reaching a depth of 2 - 15 mm.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| FI20185698A FI128299B (fi) | 2018-08-27 | 2018-08-27 | Menetelmä ylieutektoidisen terästuotteen valmistamiseksi termomekaanisella käsittelyllä |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| EP3617333A1 true EP3617333A1 (fr) | 2020-03-04 |
Family
ID=68289769
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| EP19193739.0A Withdrawn EP3617333A1 (fr) | 2018-08-27 | 2019-08-27 | Procédé de fabrication d'un produit d'acier hypereutectoïde par traitement thermomécanique |
Country Status (2)
| Country | Link |
|---|---|
| EP (1) | EP3617333A1 (fr) |
| FI (1) | FI128299B (fr) |
Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3178324A (en) | 1963-06-03 | 1965-04-13 | United States Steel Corp | Method of producing ultrafine grained steel |
| US3459599A (en) | 1966-10-17 | 1969-08-05 | United States Steel Corp | Method of thermomechanically annealing steel |
| SU456841A1 (ru) | 1973-03-02 | 1975-01-15 | Институт Металлургии Им.50-Летия Ссср Ан Грузинской Сср | Способ обработки железо-углеродистых сплавов |
| US4030944A (en) * | 1976-04-15 | 1977-06-21 | Ceskoslovenska Akademie Ved | Production of annular products from centrifugally cast steel structures |
| GB1495431A (en) * | 1974-11-18 | 1977-12-21 | Mitsubishi Heavy Ind Ltd | Method of toughening metallic material |
| WO1983004267A1 (fr) * | 1982-05-24 | 1983-12-08 | The Board Of Trustees Of The Leland Stanford Junio | Procede de transformation eutectoide divisee et production d'aciers a teneur en carbone ultra-elevee |
| RU2048540C1 (ru) * | 1992-04-24 | 1995-11-20 | Иосиф Ошерович Хазанов | Способ обработки малолегированных заэвтектоидных сталей перлитного класса |
| EP0943693A1 (fr) * | 1998-03-16 | 1999-09-22 | Ovako Steel AB | Procédé pour un recuit doux d'un acier riche en carbon |
-
2018
- 2018-08-27 FI FI20185698A patent/FI128299B/fi active IP Right Grant
-
2019
- 2019-08-27 EP EP19193739.0A patent/EP3617333A1/fr not_active Withdrawn
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3178324A (en) | 1963-06-03 | 1965-04-13 | United States Steel Corp | Method of producing ultrafine grained steel |
| US3459599A (en) | 1966-10-17 | 1969-08-05 | United States Steel Corp | Method of thermomechanically annealing steel |
| SU456841A1 (ru) | 1973-03-02 | 1975-01-15 | Институт Металлургии Им.50-Летия Ссср Ан Грузинской Сср | Способ обработки железо-углеродистых сплавов |
| GB1495431A (en) * | 1974-11-18 | 1977-12-21 | Mitsubishi Heavy Ind Ltd | Method of toughening metallic material |
| US4030944A (en) * | 1976-04-15 | 1977-06-21 | Ceskoslovenska Akademie Ved | Production of annular products from centrifugally cast steel structures |
| WO1983004267A1 (fr) * | 1982-05-24 | 1983-12-08 | The Board Of Trustees Of The Leland Stanford Junio | Procede de transformation eutectoide divisee et production d'aciers a teneur en carbone ultra-elevee |
| RU2048540C1 (ru) * | 1992-04-24 | 1995-11-20 | Иосиф Ошерович Хазанов | Способ обработки малолегированных заэвтектоидных сталей перлитного класса |
| EP0943693A1 (fr) * | 1998-03-16 | 1999-09-22 | Ovako Steel AB | Procédé pour un recuit doux d'un acier riche en carbon |
Non-Patent Citations (1)
| Title |
|---|
| MAEHARA Y ET AL: "Superplasticity of steels and ferrous alloys", MATERIALS SCIENCE AND ENGINEERING: A, ELSEVIER, AMSTERDAM, NL, vol. 128, no. 1, 15 August 1990 (1990-08-15), pages 1 - 13, XP026026284, ISSN: 0921-5093, [retrieved on 19900815], DOI: 10.1016/0921-5093(90)90090-P * |
Also Published As
| Publication number | Publication date |
|---|---|
| FI20185698A1 (fi) | 2020-02-28 |
| FI128299B (fi) | 2020-02-28 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| KR102017553B1 (ko) | 경화능과 질화특성이 뛰어난 장수명 다이캐스팅용 열간 금형강 및 그 제조방법 | |
| KR20100135206A (ko) | 열간가공 공구강 및 이를 이용한 철강제품 | |
| KR100619841B1 (ko) | 고 실리콘/저 합금 내충격 · 내마모용 고탄성 고강도강및 그의 제조방법 | |
| KR20100135205A (ko) | 열간가공 공구강 및 이를 이용한 철강제품 | |
| JP4963479B2 (ja) | 高炭素鋼板の製造方法 | |
| JP2005530041A (ja) | 冷間加工鋼及び冷間加工工具 | |
| JPH06322482A (ja) | 高靭性高速度鋼部材およびその製造方法 | |
| EP3209806A1 (fr) | Acier traité thermomécaniquement à très haute résistance | |
| CN104651745A (zh) | 由马氏体铬钢制造塑料模具的方法以及塑料模具 | |
| JP4361686B2 (ja) | 鋼材及びその製造方法 | |
| KR20140129385A (ko) | 단단한 부품에 있어서 높은 특성을 갖는 강 | |
| CN115386789B (zh) | 钢材以及使用该钢材的钢制品 | |
| EP3617333A1 (fr) | Procédé de fabrication d'un produit d'acier hypereutectoïde par traitement thermomécanique | |
| CN111492082B (zh) | 具有优异的耐磨性的钢材及其制造方法 | |
| KR102072606B1 (ko) | 충격인성이 우수한 초고강도 공구강 및 이의 제조 방법 | |
| JP5597999B2 (ja) | 被削性に優れた冷間工具鋼 | |
| JP2018035423A (ja) | 浸炭用鋼、浸炭鋼部品及び浸炭鋼部品の製造方法 | |
| JP6683074B2 (ja) | 浸炭用鋼、浸炭鋼部品及び浸炭鋼部品の製造方法 | |
| JP6465206B2 (ja) | 熱間圧延棒線材、部品および熱間圧延棒線材の製造方法 | |
| JP4099742B2 (ja) | 溶接性および被削性に優れた工具鋼およびそれを用いた金型 | |
| JP7229827B2 (ja) | 高炭素鋼板の製造方法 | |
| JP6519226B2 (ja) | 合金工具鋼 | |
| KR100506328B1 (ko) | 냉열 복합소재 특수강 및 그 제조방법 | |
| JP2018035419A (ja) | 浸炭用鋼、浸炭鋼部品及び浸炭鋼部品の製造方法 | |
| CN112899559B (zh) | 模具用钢以及模具 |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
| AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
| AX | Request for extension of the european patent |
Extension state: BA ME |
|
| STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: THE APPLICATION IS DEEMED TO BE WITHDRAWN |
|
| 18D | Application deemed to be withdrawn |
Effective date: 20200905 |