EP4119694A1 - Rare earth-containing heat-resistant alloy steel and slab continuous casting production process therefor - Google Patents
Rare earth-containing heat-resistant alloy steel and slab continuous casting production process therefor Download PDFInfo
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- EP4119694A1 EP4119694A1 EP21800289.7A EP21800289A EP4119694A1 EP 4119694 A1 EP4119694 A1 EP 4119694A1 EP 21800289 A EP21800289 A EP 21800289A EP 4119694 A1 EP4119694 A1 EP 4119694A1
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- Prior art keywords
- rare earth
- continuous casting
- resistant alloy
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- alloy steel
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- 229910052761 rare earth metal Inorganic materials 0.000 title claims abstract description 95
- 238000009749 continuous casting Methods 0.000 title claims abstract description 85
- 150000002910 rare earth metals Chemical class 0.000 title claims abstract description 78
- 229910000851 Alloy steel Inorganic materials 0.000 title claims abstract description 63
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 48
- 238000000034 method Methods 0.000 claims abstract description 31
- 238000001816 cooling Methods 0.000 claims abstract description 19
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 16
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 14
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 13
- 229910052727 yttrium Inorganic materials 0.000 claims abstract description 12
- 230000000737 periodic effect Effects 0.000 claims abstract description 11
- 229910052729 chemical element Inorganic materials 0.000 claims abstract description 10
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 9
- 230000001590 oxidative effect Effects 0.000 claims abstract description 8
- 230000004580 weight loss Effects 0.000 claims abstract description 8
- 238000005266 casting Methods 0.000 claims description 73
- 229910000831 Steel Inorganic materials 0.000 claims description 41
- 239000010959 steel Substances 0.000 claims description 41
- 238000000227 grinding Methods 0.000 claims description 23
- 238000003756 stirring Methods 0.000 claims description 14
- 229910052757 nitrogen Inorganic materials 0.000 claims description 11
- 229910052717 sulfur Inorganic materials 0.000 claims description 11
- 239000012535 impurity Substances 0.000 claims description 10
- 239000007787 solid Substances 0.000 claims description 9
- 229910052758 niobium Inorganic materials 0.000 claims description 8
- 229910052698 phosphorus Inorganic materials 0.000 claims description 7
- 229910000859 α-Fe Inorganic materials 0.000 claims description 7
- 238000003780 insertion Methods 0.000 claims 1
- 230000037431 insertion Effects 0.000 claims 1
- 239000000126 substance Substances 0.000 abstract description 2
- 239000000956 alloy Substances 0.000 description 31
- 229910045601 alloy Inorganic materials 0.000 description 30
- 230000000052 comparative effect Effects 0.000 description 22
- 239000011651 chromium Substances 0.000 description 15
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 13
- 239000011572 manganese Substances 0.000 description 12
- 239000013078 crystal Substances 0.000 description 7
- 230000007547 defect Effects 0.000 description 7
- 229910052742 iron Inorganic materials 0.000 description 6
- 239000012071 phase Substances 0.000 description 6
- 239000002893 slag Substances 0.000 description 6
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 5
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 229910052710 silicon Inorganic materials 0.000 description 5
- 239000010703 silicon Substances 0.000 description 5
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-UHFFFAOYSA-N 0.000 description 5
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 4
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 4
- 230000008018 melting Effects 0.000 description 4
- 238000002844 melting Methods 0.000 description 4
- 239000011733 molybdenum Substances 0.000 description 4
- 229910052702 rhenium Inorganic materials 0.000 description 4
- 238000005204 segregation Methods 0.000 description 4
- 238000007711 solidification Methods 0.000 description 4
- 230000008023 solidification Effects 0.000 description 4
- 238000012360 testing method Methods 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 3
- 230000003064 anti-oxidating effect Effects 0.000 description 3
- 229910052799 carbon Inorganic materials 0.000 description 3
- 229910052593 corundum Inorganic materials 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 229910052747 lanthanoid Inorganic materials 0.000 description 3
- 239000007769 metal material Substances 0.000 description 3
- 238000007254 oxidation reaction Methods 0.000 description 3
- 238000011056 performance test Methods 0.000 description 3
- 238000011946 reduction process Methods 0.000 description 3
- 229910001845 yogo sapphire Inorganic materials 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 2
- 238000003335 Production assurance Methods 0.000 description 2
- 238000003723 Smelting Methods 0.000 description 2
- 238000010521 absorption reaction Methods 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- QDOXWKRWXJOMAK-UHFFFAOYSA-N dichromium trioxide Chemical compound O=[Cr]O[Cr]=O QDOXWKRWXJOMAK-UHFFFAOYSA-N 0.000 description 2
- 230000001747 exhibiting effect Effects 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- -1 lanthanide rare earth Chemical class 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 230000005499 meniscus Effects 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 238000005457 optimization Methods 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 238000000275 quality assurance Methods 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 229910017060 Fe Cr Inorganic materials 0.000 description 1
- 229910002544 Fe-Cr Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- BPQQTUXANYXVAA-UHFFFAOYSA-N Orthosilicate Chemical compound [O-][Si]([O-])([O-])[O-] BPQQTUXANYXVAA-UHFFFAOYSA-N 0.000 description 1
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical group O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000000969 carrier Substances 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- UPHIPHFJVNKLMR-UHFFFAOYSA-N chromium iron Chemical compound [Cr].[Fe] UPHIPHFJVNKLMR-UHFFFAOYSA-N 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- PMHQVHHXPFUNSP-UHFFFAOYSA-M copper(1+);methylsulfanylmethane;bromide Chemical compound Br[Cu].CSC PMHQVHHXPFUNSP-UHFFFAOYSA-M 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000004512 die casting Methods 0.000 description 1
- 238000007710 freezing Methods 0.000 description 1
- 230000008014 freezing Effects 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 238000007689 inspection Methods 0.000 description 1
- 150000002602 lanthanoids Chemical class 0.000 description 1
- 229910052746 lanthanum Inorganic materials 0.000 description 1
- FZLIPJUXYLNCLC-UHFFFAOYSA-N lanthanum atom Chemical compound [La] FZLIPJUXYLNCLC-UHFFFAOYSA-N 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 230000003137 locomotive effect Effects 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000000691 measurement method Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000005121 nitriding Methods 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000000746 purification Methods 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000010956 selective crystallization Methods 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 229910052814 silicon oxide Inorganic materials 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 238000009865 steel metallurgy Methods 0.000 description 1
- 238000007920 subcutaneous administration Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/16—Controlling or regulating processes or operations
- B22D11/22—Controlling or regulating processes or operations for cooling cast stock or mould
- B22D11/225—Controlling or regulating processes or operations for cooling cast stock or mould for secondary cooling
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/10—Supplying or treating molten metal
- B22D11/11—Treating the molten metal
- B22D11/114—Treating the molten metal by using agitating or vibrating means
- B22D11/115—Treating the molten metal by using agitating or vibrating means by using magnetic fields
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/12—Accessories for subsequent treating or working cast stock in situ
- B22D11/1206—Accessories for subsequent treating or working cast stock in situ for plastic shaping of strands
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/16—Controlling or regulating processes or operations
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/16—Controlling or regulating processes or operations
- B22D11/18—Controlling or regulating processes or operations for pouring
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/16—Controlling or regulating processes or operations
- B22D11/20—Controlling or regulating processes or operations for removing cast stock
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/16—Controlling or regulating processes or operations
- B22D11/20—Controlling or regulating processes or operations for removing cast stock
- B22D11/201—Controlling or regulating processes or operations for removing cast stock responsive to molten metal level or slag level
- B22D11/205—Controlling or regulating processes or operations for removing cast stock responsive to molten metal level or slag level by using electric, magnetic, sonic or ultrasonic means
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
-
- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- 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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- 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
- C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
Abstract
Description
- The present invention relates to a metal material and a manufacturing method thereof, in particular to a rare earth-bearing heat-resistant alloy steel and a continuous casting production process therefor.
- In industrial production, heat-resistant alloys have been produced for many years, and many well-known foreign metallurgical enterprises produce heat-resistant alloys. The heat-resistant alloys have the advantages of high aperture ratio, large specific surface area, low heat capacity, high thermal conductivity and high strength. The heat-resistant alloys can be used as main raw materials for metal carriers in an exhaust gas purification device, and are widely used in automobiles, diesel locomotives, motorcycles, small general machinery and other industries.
- A rare earth-bearing heat-resistant alloy is a material with Fe, Cr and Al as the matrix and adding some alloys such as Mo, Cu, Nb, V and mixed rare earths, which can improve high-temperature performance, electrical resistivity and grain refinement. For the smelting process for the rare earth-bearing heat-resistant alloys, die casting and electroslag processes are mainly used at present, and continuous casting process is used in a few cases, followed by hot rolling and cold rolling.
- In the iron and steel metallurgy industry around the world, with the continuous casting technology being gradually applied to the production of special steels, some enterprises have used slab continuous caster to produce special alloy products. However, the rare earth-bearing heat-resistant alloys are prone to precipitation of brittle phases during the cooling process of continuous casting, resulting in the formation of cracks and inclusion defects in the continuous casting slabs.
- One of the objectives of the present invention is to provide a rare earth-bearing heat-resistant alloy steel, which has an electrical resistivity of 1.3-1.5 µΩ•m at room temperature, can withstand an applicable temperature of 1000-1300 °C, and has an elongation of 5-25% and an oxidative weight loss of 0.2-8.0 g/(cm2•h) at the applicable temperature of 1000-1300 °C, thus exhibiting good quality and excellent heat resistance.
- In order to achieve the above-mentioned objective, the present invention provides a rare earth-bearing heat-resistant alloy steel, which comprises the following chemical elements in mass percentage:
0<C≤0.05%, 0<Si≤1.0%, 0<Mn≤1.0%, Cr: 13.0-28.0%, Al: 2.0-8.0%, 0<Nb≤0.50%, 0<Co≤0.50%, Mo: 0.5-6.0%, Y: 0.01-0.2%, and at least one of rare earth elements Nos. 57 to 71 in Periodic Table of Elements: 0.01-0.1%. - The expression "at least one of rare earth elements Nos. 57 to 71 in Periodic Table of Elements: 0.01-0.1%" means that: when the alloy steel comprises one of the rare earth elements Nos. 57 to 71, the content of the rare earth element is 0.01-0.1%; and when the alloy steel comprises more than one of the rare earth elements Nos. 57 to 71, the total content of these rare earth elements is 0.01-0.1%.
- Preferably, in the rare earth-bearing heat-resistant alloy steel of the present invention, the content of chemical elements in mass percentage is as follows:
0<C≤0.05%, 0<Si≤1.0%, 0<Mn≤1.0%, Cr: 13.0-28.0%, Al: 2.0-8.0%, 0<Nb≤0.50%, 0<Co≤0.50%, Mo: 0.5-6.0%, Y: 0.01-0.2%, at least one of rare earth elements Nos. 57 to 71 in Periodic Table of Elements: 0.01-0.1%, and the balance being Fe and inevitable impurities. - In the rare earth-bearing heat-resistant alloy steel of the present invention, the design principles of each chemical element are as follows:
C: In the rare earth-bearing heat-resistant alloy steel of the present invention, carbon can increase the electrical resistance of the steel and increase the strength of the steel. - However, it should be noted that carbon is prone to be austenitized, which tends to form carbide precipitates with Cr, thereby reducing the service life of the steel. Therefore, the less content of carbon in steel, the property will be better. In the rare earth-bearing heat-resistant alloy steel of the present invention, the content of C in mass percentage is controlled to be 0<C≤0.05%.
- In some preferred embodiments, the content of C in mass percentage can be controlled to be 0.01≤C≤0.05%.
- In some more preferred embodiments, the content of C in mass percentage can be controlled to be 0.01≤C≤0.03%.
- Si: In the rare earth-bearing heat-resistant alloy steel of the present invention, silicon is generally brought in by the raw materials and alloy materials. A high content of silicon in the steel will increase electrical resistance and room-temperature strength; the anti-oxidation effect of silicon at a medium temperature can reduce the loss of aluminum and rare earth; and silicon can reduce nitrogen absorption at a high temperature. However, it should be noted that silicate inclusions will adversely affect the alloy matrix. Especially in a high-temperature anti-oxidation film composition, if there is silicon oxide, the integrity of an Al2O3 oxide film will be affected. Therefore, the silicon content should not be too high. In the rare earth-bearing heat-resistant alloy steel of the present invention, the content of Si in mass percentage is controlled to be 0<Si≤1.0%.
- In some preferred embodiments, the content of Si in mass percentage can be controlled to be 0.02≤Si≤1.0%.
- In some more preferred embodiments, the content of Si in mass percentage can be controlled to be 0.2≤Si≤0.5%.
- Mn: In the rare earth-bearing heat-resistant alloy steel of the present invention, manganese can increase the toughness of the steel, and is prone to be austenitized. However, it should be noted that manganese can form oxides with a low melting point in the rare earth-bearing heat-resistant alloy steel, thereby reducing the thermal stability of the alloy. Therefore, in the rare earth-bearing heat-resistant alloy steel of the present invention, the content of Mn in mass percentage is controlled to be 0<Mn≤1.0%.
- In some preferred embodiments, the content of Mn in mass percentage can be controlled to be 0.05≤Mn≤1.0%.
- In some more preferred embodiments, the content of Mn in mass percentage can be controlled to be 0.2≤Mn≤0.4%.
- Cr: In the rare earth-bearing heat-resistant alloy steel of the present invention, chromium and iron have many properties that are not very different, both of which are body-centered cubic lattices, and their lattice constants are similar. The chromium content in ferrite stainless steel is usually not less than 13%. The addition of chromium to iron can greatly increase the electrical resistivity of iron, and the electrical resistivity of iron will increase rapidly with the increasing content of Cr. However, it should be noted that when the content of chromium in the steel exceeds 28%, a σ brittle phase will precipitate and a hardening phase will be dissolved, and the electrical resistivity will gradually decrease. At the same time, the addition of chromium will cause the strength of the steel to improve rapidly and the brittleness of the steel to increase continuously. Therefore, in the rare earth-bearing heat-resistant alloy steel of the present invention, the content of Cr in mass percentage is controlled to be 13.0-28.0%.
- In some preferred embodiments, the content of Cr in mass percentage can be controlled to be 17.0-25.0%.
- Al: In the rare earth-bearing heat-resistant alloy steel of the present invention, when the content of aluminum in the Fe-Cr alloy is not less than 2%, the anti-oxidation performance will be improved; especially at a high temperature, an oxide film composition can be transformed from Cr2O3 to Al2O3, so that an oxide film is more stable and firmer, which greatly increases the applicable temperature and prolongs the service life. However, it should be noted that the addition of aluminum will increase the brittleness of the alloy steel. When the content of Al in the steel exceeds 8%, it is difficult to carry out both cold and hot workability. Therefore, in the rare earth-bearing heat-resistant alloy steel of the present invention, the content of Al in mass percentage is controlled to be 2.0-8.0%.
- In some preferred embodiments, the content of Al in mass percentage can be controlled to be 3.0-6.0%.
- Nb: In the rare earth-bearing heat-resistant alloy steel of the present invention, Nb can improve the high-temperature strength, reduce high-temperature creep, and prolong the service life of the rare earth-bearing heat-resistant alloy steel. However, considering that the cost and the production difficulty will increase as the content of Nb increases, the content of Nb in mass percentage in the rare earth-bearing heat-resistant alloy steel of the present invention is controlled to be 0<Nb≤0.50%.
- In some preferred embodiments, the content of Nb in mass percentage can be controlled to be 0<Nb≤0.40%.
- In some more preferred embodiments, the content of Nb in mass percentage can be controlled to be 0.02≤Nb≤0.40%.
- In the most preferred embodiment, the content of Nb in mass percentage can be controlled to be 0.05≤Nb≤0.40%.
- Co: In the rare earth-bearing heat-resistant alloy steel of the present invention, Co has similar effect with Nb, and Co can also increase the high-temperature strength, reduce high-temperature creep, and prolong the service life of the rare earth-bearing heat-resistant alloy. Similarly, considering that the production cost and the production difficulty will increase as the content of Co increases, the content of Co in mass percentage in the rare earth-bearing heat-resistant alloy steel of the present invention is controlled to be 0<Co≤0.50%.
- In some preferred embodiments, the content of Co in mass percentage can be controlled to be 0<Co≤0.20%.
- In some more preferred embodiments, the content of Co in mass percentage can be controlled to be 0.01≤Co≤0.20%.
- In the most preferred embodiment, the content of Co in mass percentage can be controlled to be 0.05≤Nb≤0.20%.
- Mo, Y: In the rare earth-bearing heat-resistant alloy steel of the present invention, a small amount of molybdenum (Mo) and yttrium (Y) are added. Molybdenum can effectively reduce the high-temperature creep rate and prolong the service life of the steel. Yttrium can refine alloy grains, thereby improving the room-temperature strength and high-temperature strength of the steel, and reducing the brittleness. The affinity of yttrium to oxygen is between that of lanthanum and that of aluminum, and it can form an enamel-like oxide film, thereby improving the high-temperature oxidation resistance and the nitriding resistance of the alloy steel. Like molybdenum, yttrium can effectively reduce the high-temperature creep rate and prolong the service life of the steel. However, it should be noted that when the content of molybdenum in the steel is too high, it is difficult to perform both hot and cold machining. When pickling the oxide scales, peeling or overwashing is common. Correspondingly, it tends to burn during smelting when the content of yttrium in the steel is too high. Therefore, in the rare earth-bearing heat-resistant alloy steel of the present invention, the content of Mo in mass percentage is controlled to be 0.5-6.0%, and the content of Y in mass percentage is controlled to be 0.01-0.2%.
- In some preferred embodiments, the content of Mo in mass percentage can be controlled to be 1.5-5.0%, and the content of Y in mass percentage can be controlled to be 0.05-0.15%.
- It should be noted that in the rare earth-bearing heat-resistant alloy steel of the present invention, the present inventors use lanthanide rare earth elements Nos. 57 to 71 while using Y, which mainly play the role of significantly prolonging the service life. A larger added content of rare earths indicates a higher service life value. However, in practical production, if more rare earths are added, more rare earths will be burned, and the possibility of increasing impurities and hydrogen absorption will be larger, while the increase in the residual content of rare earths in the alloy after burning is less. When the amount of the lanthanide rare earth added in the alloy is greater than 0.1%, the service life value of the steel shows a downward trend. Furthermore, the cost of the lanthanide rare earth is high, and the content should not be too high. Therefore, in the rare earth-bearing heat-resistant alloy steel of the present invention, the added content of at least one of rare earth elements Nos. 57 to 71 in Periodic Table of Elements in mass percentage is controlled to be 0.01-0.1%.
- Preferably, the content of at least one of rare earth elements Nos. 57 to 71 in Periodic Table of Elements in mass percentage can be controlled to be 0.02-0.05%.
- Preferably, in the rare earth-bearing heat-resistant alloy steel of the present invention, the content of Nb and Co in mass percentage further satisfies: Nb+Co≤0.50%, which can increase the high-temperature strength, reduce the high-temperature creep, and prolong the service life of the rare earth-bearing heat-resistant alloy. In case of Nb+Co>0.5%, the continuous casting production is difficult, the crack sensitivity is high, and the alloy cost is increased. Nb and Co in the formula represent the content of each corresponding element in mass percentage respectively.
- Preferably, in the rare earth-bearing heat-resistant alloy steel of the present invention, in the inevitable impurities, the content of P, S and N satisfies at least one of: P≤0.040%, S≤0.020%, and N≤0.020%.
- Preferably, in the rare earth-bearing heat-resistant alloy steel of the present invention, in the inevitable impurities, the content of P, S and N satisfies at least one of: P≤0.020%, S≤0.010%, and N≤0.010%.
- In the above technical solution, in the rare earth-bearing heat-resistant alloy steel of the present invention, P, N and S are all inevitable impurity elements in the steel, and the content of these impurity elements in the steel should not be too high. Both P and S can generate brittle substances with a low melting point, which tend to cause hot brittleness. Correspondingly, if the content of N in the rare earth-bearing heat-resistant alloy steel is too high, brittle aluminum nitride will be formed, which tend to cause brittle fracture and hinder the formation of Al2O3 oxide film.
- Preferably, in the rare earth-bearing heat-resistant alloy steel of the present invention, the content of chemical elements in mass percentage satisfies at least one of: 0.01≤C≤0.03%, 0.2≤Si≤0.5%, 0.2≤Mn≤0.4%, Cr: 17.0-25.0%, Al: 3.0-6.0%, 0<Nb≤0.40%, 0<Co≤0.20%, Mo: 1.5-5.0%, Y: 0.05-0.15%, and at least one of rare earth elements Nos. 57 to 71 in Periodic Table of Elements: 0.02-0.05%.
- Preferably, in the rare earth-bearing heat-resistant alloy steel of the present invention, the main microstructure is ferrite.
- Preferably, the properties of the rare earth-bearing heat-resistant alloy steel of the present invention satisfy at least one of: being able to withstand an applicable temperature of 1000-1300 °C; having an elongation of 5-25% and an oxidative weight loss of 0.2-8.0 g/(cm2•h) at the applicable temperature of 1000-1300 °C; and having an electrical resistivity of 1.3-1.5 µΩ•m at room temperature.
- Correspondingly, another objective of the present invention is to provide a slab continuous casting production process for rare earth-bearing heat-resistant alloy steel. The slab continuous casting production process can effectively improve the quality of the continuous casting slab, and the produced continuous casting slab has excellent characteristics of good quality on a surface and center of the continuous casting slab. It can fully exert the advantages of continuous casting production, can effectively suppress recesses and cracks of the casting slab, significantly improve the surface and center quality of the casting slab and achieve sequence casting. The slab continuous casting production process of the present invention is a key technology for achieving continuous casting production and quality assurance of rare earth-bearing heat-resistant alloy slabs, and has extremely high promotion and application value for the development of rare-earth-bearing varieties and optimization of the process for enterprises that use a continuous casting process to achieve production and testing. It can not only increase production capacity, and but also effectively reduce production cost, so that the comprehensive competitiveness of an enterprise is greatly enhanced.
- In order to achieve the above objectives, the present invention provides the above-mentioned slab continuous casting production process for the rare earth-bearing heat-resistant alloy steel. In the continuous casting process, the specific water ratio of secondary cooling is controlled to be 1.02±0.10 L/kg.
- In the slab continuous casting production process of the present invention, a structure of rare earth-bearing heat-resistant alloy after solidification is mainly ferrite, and the columnar crystals are developed. Through a large number of experiments, the inventors have found that if weak cooling is used, the solidification time will be long, the columnar crystals will fully grow, and transgranular structure will appear in the casting slab at a low magnification, resulting in crack defects after rolling. In the slab continuous casting production process of the present invention, the present inventors have designed that: a strong cooling process is performed on the rare earth-bearing heat-resistant alloy steel in the secondary cooling zone, wherein when the specific water ratio of secondary cooling is controlled to be 1.02±0.10 L/kg, the lengths of primary columnar crystal and the spacing of secondary columnar crystals are the shortest, which are the prerequisites for improving the internal quality of the casting slab; and the electromagnetic stirring and soft reduction process of the present invention is further used to further ensure the internal quality of the casting slab. In some preferred embodiments, in the continuous casting process, the specific water ratio of secondary cooling can be controlled to be 1.02±0.06 L/kg, and the Mannesmann rating of the casting slab at low magnification is M1.7-2.0.
- Preferably, in the slab continuous casting production process of the present invention, in the continuous casting step, a temperature for hot grinding the casting slab is controlled to be 100-600 °C.
- In the slab continuous casting production process of the present invention, the surface of the continuous casting slab of the rare earth-bearing heat-resistant alloy steel will have defects such as local recesses, slag pits and deep vibration marks in different degrees. These defects will affect the surface quality of subsequent hot-rolled and cold-rolled products. At the same time, considering that the brittle phase is precipitated in the cooling process for the rare earth-bearing heat-resistant alloy steel, a hot grinding process can be used for the casting slab to effectively alleviate the above defects.
- However, it should be noted that if the temperature in the hot grinding process is lower than 100 °C, the precipitated brittle phase tends to cause grinding cracks; and if the temperature is higher than 600 °C, it will exceed the capacity of the grinding equipment. Therefore, in the slab continuous casting production process of the present invention, the temperature for hot grinding the casting slab is controlled to be 100-600 °C. In some preferred embodiments, in the slab continuous casting production process of the present invention, the temperature for hot grinding the casting slab can be controlled to be 300-500 °C.
- Preferably, in the slab continuous casting production process of the present invention, process parameters of the continuous casting process are controlled to satisfy at least one of:
- the specific water ratio of secondary cooling is controlled to be 1.02±0.06 L/kg;
- the temperature for hot grinding the casting slab is 300-500 °C;
- the electromagnetic stirring current is 1000-2000 A;
- the soft reduction amount is 3-10 mm;
- the solid fraction fs of the casting slab center corresponding to a reduction zone is 0.10-0.90;
- the grinding amount on one casting slab side is 3-10 mm;
- the superheat degree of molten steel in a tundish is controlled to be 10-50 °C;
- the average casting speed of continuous casting is controlled to be 0.40-1.50 m/min; and
- the submerged depth of a continuous casting crystallizer nozzle is controlled to be 90-130 mm.
- In the slab continuous casting production process of the present invention, in order to improve the segregation problem that may be possibly caused by the ferrite in the rare earth-bearing heat-resistant alloy during the continuous casting process, an electromagnetic stirring in the secondary cooling zone and dynamic soft reduction process can be added in the slab continuous casting production process of the present invention.
- When the electromagnetic stirring in the secondary cooling zone and dynamic soft reduction process are used, if the current of electromagnetic stirring is less than 1000 A, and the soft reduction amount is less than 3 mm, it will not be effective in improving the quality of the center of a ferrite slab. If the current of electromagnetic stirring is higher than 2000 A, a liquid level of the crystallizer fluctuates greatly, and the slab is prone to negative segregation. If the soft reduction amount is greater than 10 mm, the narrow side of the casting slab is prone to bulge, and intermediate cracks are prone to be generated in the casting slab. In the ferrite structure of the rare earth-bearing heat-resistant alloy, the columnar crystals are developed; and through a lot of experiments, the results have shown that dynamic soft reduction is suitable for the whole solidification process of the two-phase region. Therefore, in the slab continuous casting production process of the present invention, the current of electromagnetic stirring is controlled to be 1000-2000 A, the soft reduction amount is controlled to be 3-10 mm, and the solid fraction fs of the casting slab center corresponding to a reduction zone is controlled to be 0.10-0.90. If fs corresponding to the reduction zone is less than 0.10, which is equivalent to complete liquid phase reduction, the columnar crystals have not been completely formed, and the effect of improving segregation is not obvious. If fs corresponding to the reduction zone is more than 0.90, the casting slab being nearly completely solidified, the columnar crystals cannot be completely crushed by reduction, and there is risk of internal cracks. Thus, the solid fraction fs in the center of the casting slab corresponding to the reduction zone being 0.10-0.90 is an important condition to control the Mannesmann rating of the casting slab at low magnification to be M1.7-2.0. In some preferred embodiments, the electromagnetic stirring current can be controlled to be 1400-2000 A, the soft reduction amount can be controlled to be 6-9 mm, and the solid fraction fs of the casting slab center corresponding to the reduction zone can be controlled to be 0.20-0.90.
- In addition, it should be noted that when grinding the casting slab, if the grinding amount on one casting slab side is less than 3 mm, the defects may not be completely removed. If the grinding amount on one side is greater than 10 mm, the yield of the casting slab will be affected. Therefore, in the slab continuous casting production process of the present invention, the grinding amount on one casting slab side can be controlled to be 3-10 mm. In some preferred embodiments, the grinding amount on one casting slab side can be controlled to be 5-8 mm.
- In the continuous casting process, if the superheat degree of molten steel is lower than 10 °C, the fluidity of the molten steel is poor, which will easily lead to the freezing of steel at the crystallizer nozzle to force pouring to be interrupted, and the melting effect of covering slag is not good. If the superheat degree of molten steel is higher than 50 °C, the rare earth-bearing heat-resistant alloy steel is prone to segregation, resulting in long solidification time and sufficient selective crystallization, which will exacerbate the quality issues of the casting slab. Therefore, in the slab continuous casting production process of the present invention, the superheat degree of molten steel in the tundish is controlled to be 10-50 °C. In some preferred embodiments, the superheat degree of molten steel in the tundish can be controlled to be 15-30 °C.
- In addition, in the continuous casting process, if the average casting speed of continuous casting is faster than 1.50 m/min, the initial slab shell is thin, and the slab cooling is uneven, which tend to cause longitudinal cracks and even bleed-out. If the average casting speed of continuous casting is slower than 0.40 m/min, the cooling time of the slab in the crystallizer is too long, the molten steel at the meniscus is in a low-temperature state and the melting effect of the covering slag is not good, which tend to cause cracks and affect the overall production capacity of the continuous caster. Therefore, in the slab continuous casting production process of the present invention, the average casting speed of continuous casting is controlled to be 0.40-1.50 m/min. In some preferred embodiments, the average casting speed of continuous casting can be controlled to be 0.80-1.2 m/min.
- Correspondingly, in the continuous casting process, if the submerged depth of the crystallizer nozzle is too shallow, the impact of the nozzle stream on the steel slag interface will be too strong, which will increase the probability of reaction between the molten steel and covering slag in the crystallizer, and increase the probability of slag entrapment on the meniscus. If the submerged depth of the crystallizer nozzle is too deep, the casting slab is prone to cracks. Therefore, in the slab continuous casting production process of the present invention, the submerged depth of the continuous casting crystallizer nozzle is controlled to be 90-130 mm. In some preferred embodiments, the submerged depth of the continuous casting crystallizer nozzle can be controlled to be 100-125 mm.
- Preferably, in the slab continuous casting production process of the present invention, the process parameters of the continuous casting process are controlled to satisfy at least one of:
- the electromagnetic stirring current is 1400-2000 A;
- the soft reduction amount is 6-9 mm;
- the solid fraction fs of casting slab center corresponding to a reduction zone is 0.20-0.90;
- the grinding amount on one casting slab side is 5-8 mm;
- the superheat degree of molten steel in the tundish is controlled to be 15-30 °C;
- the average casting speed of continuous casting is controlled to be 0.80-1.2 m/min; and
- the submerged depth of the continuous casting crystallizer nozzle is controlled to be 100-125 mm.
- Compared with the prior art, the rare earth-bearing heat-resistant alloy steel and the slab continuous casting production process therefor according to the present invention have the following advantages and beneficial effects:
The rare earth-bearing heat-resistant alloy steel of the present invention has an electrical resistivity of 1.3-1.5 µΩ•m at room temperature, can withstand an applicable temperature of 1000-1300 °C, and has an elongation of 5-25% and an oxidative weight loss of 0.2-8.0 g/(cm2•h) at the applicable temperature of 1000-1300 °C, exhibiting good quality and excellent properties. - In addition, the slab continuous casting production process for the rare earth-bearing heat-resistant alloy steel of the present invention can effectively improve the quality of a continuous casting slab. The produced continuous casting slab has excellent characteristics such as good quality on the surface and center of the continuous casting slab. It can fully exert the advantages of continuous casting production, can effectively suppress the occurrence of recesses and cracks of the casting slab, significantly improve the surface and center quality of the casting slab and achieve sequence casting. The slab continuous casting production process of the present invention is a key technology for realizing continuous casting production and quality assurance of rare earth-bearing heat-resistant alloy slabs, and has extremely high promotion and application value for the development of rare-earth-bearing varieties and optimization of the process for enterprises that use a continuous casting process to achieve production and testing. It not only increases production capacity, and but also effectively reduces production cost, so that the comprehensive competitiveness of an enterprise can be greatly enhanced.
- The rare earth-bearing heat-resistant alloy steel and the slab continuous casting production process therefor according to the present invention will be further explained and illustrated below in combination with specific embodiments. However, the technical solution of the present disclosure is not limited to the explanation and illustration.
- Table 1 shows the content of chemical elements in mass percentage in rare earth-bearing heat-resistant alloy steels in Inventive Examples 1-6 and Comparative Examples 1-4.
Table 1 (wt%, the balance being Fe and inevitable impurities other than P, S and N) No. Chemical elements c Si Mn Cr Al Nb Co Mo Y P S N Re Nb+Co Inventive Example 1 0.01 0.38 0.27 22.3 4.7 0.19 0.01 3.5 0.1 0.017 0.001 0.008 0.03 0.20 Inventive Example 2 0.012 0.53 0.05 28.0 2.0 0.23 0.15 3.0 0.13 0.011 0.001 0.010 0.10 0.38 Inventive Example 3 0.015 0.35 0.3 17.2 5.4 0.02 0.10 2.0 0.2 0.016 0.002 0.013 0.01 0.12 Inventive Example 4 0.02 1.0 1.0 13.0 8.0 0.50 0.02 3.5 0.09 0.014 0.002 0.002 0.025 0.52 Inventive Example 5 0.03 0.02 0.65 21.2 3.2 0.03 0.50 6.0 0.01 0.020 0.001 0.005 0.072 0.53 Inventive Example 6 0.05 0.25 0.12 19.6 2.8 0.02 0.06 0.5 0.017 0.007 0.001 0.007 0.015 0.08 Comparative Example 1 0.01 0.40 0.27 12 1.0 0.10 0.10 0.1 0.16 0.010 0.001 0.008 0 0.20 Comparative Example 2 0.02 0.8 0.50 8 1.8 0.05 0.05 0.4 0.12 0.008 0.002 0.003 0.008 0.10 Comparative Example 3 0.03 0.2 0.72 20 8.2 0.55 0.8 3.3 0.08 0.020 0.001 0.004 0.21 1.35 Comparative Example 4 0.04 0.35 0.8 15.6 9.8 0.61 0.63 2.3 0.03 0.007 0.001 0.009 0.25 1.24 - It should be noted that Re in Inventive Examples 1-6 and Comparative Examples 1-4 in Table 1 represents the content of any one element or the total content of several elements among elements Nos. 57 to 71 in Periodic Table of Elements in mass percentage.
- The rare earth-bearing heat-resistant alloy steels of Inventive Examples 1-6 of the present invention and Comparative Examples 1-4 were prepared by the following continuous casting production process:
In the continuous casting process, firstly, the superheat degree of molten steel in the continuous casting tundish was controlled to be 10-50 °C and the submerged depth of the continuous casting crystallizer nozzle was controlled to be 90-130 mm. Then continuous casting pouring was started, wherein the average casting speed was controlled to be 0.40-1.50 m/min and the specific water ratio of secondary cooling was controlled to be 1.02±0.10 L/kg. After the casting slab entered the secondary cooling zone, electromagnetic stirring was started. The electromagnetic stirring current was 1000-2000 A, the soft reduction amount was controlled to be 3-10 mm, and the solid fraction fs of the casting slab center corresponding to the reduction zone was controlled to be 0.10-0.90. Finally, after the casting slab was released from the caster, the temperature for hot grinding the casting slab was controlled to be 100-600 °C, and the grinding amount on one casting slab side was controlled to be 3-10 mm. - Table 2 shows specific process parameters of manufacturing methods of the rare earth-bearing heat-resistant alloy steels of Inventive Examples 1-6 and Comparative Examples 1-4.
Table 2 No. Sectional dimension of slab (mm) Specific water ratio of secondary cooling (L/kg) Temperature for hot grinding (°C) Electromagnetic stirring current (A) Soft reduction amount (mm) Solid fraction fs of casting slab center corresponding to reduction zone Grinding amount on one casting slab side (mm) Average superheat degree of molten steel in tundish (°C) Average casting speed of continuous casting (m/min) Submerged depth of continuous casting crystallizer nozzle (mm) Inventive Example 1 250×1200 0.96 450 1600 8.0 0.1-0.9 8 26 0.76 120 Inventive Example 2 200×1140 0.98 330 1400 6.5 0.1-0.9 7 32 0.92 105 Inventive Example 3 150×1300 1.08 200 1200 4.5 0.1-0.9 3 12 1.2 120 Inventive Example 4 200×1250 1.02 350 2000 7.0 0.1-0.9 5 39 1.0 125 Inventive Example 5 150×1450 1.12 280 1000 3.5 0.1-0.9 4 33 1.5 115 Inventive Example 6 230×1080 0.92 570 1800 9.0 0.1-0.9 10 47 0.4 90 Comparative Example 1 150×1000 1.10 550 1200 5.0 0.1-0.9 3 18 1.4 120 Comparative Example 2 200×1200 1.00 450 1600 6.0 0.1-0.9 5 26 1.2 125 Comparative Example 3 250×1350 0.94 250 2000 8.5 0.1-0.9 7 40 0.8 105 Comparative Example 4 230×1100 0.96 300 1800 7.5 0.1-0.9 6 30 1.0 95 - Various performance tests were performed on the rare earth-bearing heat-resistant alloy steels of Inventive Examples 1-6 and Comparative Examples 1-4, and the test results were listed in Table 3. Performance test methods: GB/T 4338-2006 "Metallic materials - Tensile Testing at elevated temperature"; GB/T 13303-1991 "Steels - Determination method of oxidation resistance"; GB/T 351-2019 "Metallic materials - Resistivity measurement method"; and "Mannesmann Demark Steel Corporation - Standard and method for inspection of defects of continuous casting slab".
- Table 3 shows the performance test results of the rare earth-bearing heat-resistant alloy steels of Inventive Examples 1-6 and Comparative Examples 1-4.
Table 3 No. Elongation at applicable temperature of 1000-1300 °C (%) Oxidative weight loss at applicable temperature of 1000-1300 °C g/(cm2·h) Electrical resistivity at room temperature (µΩ·m) Quality of casting slab Inventive Example 1 17.3 0.46 1.303 No cracks, casting slab rating at low magnification of M1.8 Inventive Example 2 24.7 7.98 1.446 No cracks, casting slab rating at low magnification of M2.0 Inventive Example 3 13.5 0.37 1.444 No cracks, casting slab rating at low magnification of M1.7 Inventive Example 4 5.1 0.22 1.499 No cracks, casting slab rating at low magnification of M2.0 Inventive Example 5 20.1 2.33 1.496 No cracks, casting slab rating at low magnification of M2.0 Inventive Example 6 22.7 6.55 1.461 No cracks, casting slab rating at low magnification of M2.0 Comparative Example 1 8.2 9.7 1.232 No cracks, casting slab rating at low magnification of M1.8 Comparative Example 2 11.6 10.1 1.195 No cracks, casting slab rating at low magnification of M1.9 Comparative Example 3 3.4 0.9 1.356 Cracks, casting slab rating at low magnification of M2.4 Comparative Example 4 2.8 2.9 1.421 Cracks. casting slab rating at low magnification of M2.2 - It can be seen from Table 3 that the rare earth-bearing heat-resistant alloy steel of each Inventive Example of the present invention had an electrical resistivity of 1.3-1.5 µΩ•m at room temperature, was able to withstand an applicable temperature of 1000-1300 °C, and had an elongation of 5-25% at the applicable temperature of 1000-1300 °C. Test results on oxidization resistance of alloys showed that the oxidative weight loss in each Inventive Example at the applicable temperature of 1000-1300 °C was 0.2-8.0 g/(cm2•h). Thus, the rare earth-bearing heat-resistant alloy steels in Inventive Examples exhibited excellent heat resistance. Furthermore, the casting slab in each Inventive Example of the present invention exhibited good quality, had no cracks, and had a Mannesmann rating at low magnification of M1.7-2.0.
- In Comparative Examples 1 and 2, the contents of Al, Cr, Mo and Re were lower than the claimed ranges of the present invention, and the "Oxidative weight loss at applicable temperature of 1000-1300 °C" and the "Electrical resistivity at room temperature" in the heat resistance properties did not satisfy the requirements. In Comparative Examples 3 and 4, the contents of Al, Co, Nb and Re were higher than the claimed ranges of the present invention, the "Elongation at applicable temperature of 1000-1300 °C" was less than 5%, and the rating of casting slab at low magnification exceeded M2.0. In Comparative Examples 3 and 4, the contents of Al and Re were high, such that the casting slabs were prone to subcutaneous inclusions, which would become the source of cracks in the continuous casting slab; and the contents of Co and Nb were high, such that the casting slabs fell into the third brittle zone in the high-temperature range, which would increase the crack susceptibility of the casting slab. Therefore, when the contents of Al, Co, Nb and Re were higher than the claimed ranges of the present invention, the casting slab exhibited low quality.
- It should be noted that the above-listed examples are only specific embodiments of the present disclosure. Apparently, the present disclosure is not limited to the above embodiments, and similar variations or modifications that are directly derived or easily conceived from the present disclosure by those skilled in the art should fall within the scope of the present disclosure.
Claims (12)
- A rare earth-bearing heat-resistant alloy steel, comprising the following chemical elements in mass percentage:
0<C≤0.05%, 0<Si≤1.0%, 0<Mn≤1.0%, Cr: 13.0-28.0%, Al: 2.0-8.0%, 0<Nb≤0.50%, 0<Co≤0.50%, Mo: 0.5-6.0%, Y: 0.01-0.2%, and at least one of rare earth elements Nos. 57 to 71 in Periodic Table of Elements: 0.01-0.1%. - The rare earth-bearing heat-resistant alloy steel as claimed in claim 1, wherein the content of chemical elements in mass percentage is as follows:
0<C≤0.05%, 0<Si≤1.0%, 0<Mn≤1.0%, Cr: 13.0-28.0%, Al: 2.0-8.0%, 0<Nb≤0.50%, 0<Co≤0.50%, Mo: 0.5-6.0%, Y: 0.01-0.2%, at least one of rare earth elements Nos. 57 to 71 in Periodic Table of Elements: 0.01-0.1%, and the balance being Fe and inevitable impurities. - The rare earth-bearing heat-resistant alloy steel as claimed in claim 1 or 2, wherein the content of Nb and Co in mass percentage further satisfies: Nb+Co≤0.50%.
- The rare earth-bearing heat-resistant alloy steel as claimed in claim 2, wherein in the inevitable impurities, the content of P, S and N satisfies at least one of: P≤0.040%, S≤0.020%, and N≤0.020%.
- The rare earth-bearing heat-resistant alloy steel as claimed in claim 2, wherein in the inevitable impurities, the content of P, S and N satisfies at least one of: P≤0.020%, S≤0.010%, and N≤0.010%.
- The rare earth-bearing heat-resistant alloy steel as claimed in claim 1 or 2, wherein the content of chemical elements in mass percentage satisfies at least one of:
0.01≤C≤0.03%, 0.2≤Si≤0.5%, 0.2≤Mn≤0.4%, Cr: 17.0-25.0%, Al: 3.0-6.0%, 0<Nb≤0.40%, 0<Co≤0.20%, Mo: 1.5-5.0%, Y: 0.05-0.15%, and at least one of rare earth elements Nos. 57 to 71 in Periodic Table of Elements: 0.02-0.05%. - The rare earth-bearing heat-resistant alloy steel as claimed in claim 1 or 2, wherein a microstructure of the rare earth-bearing heat-resistant alloy steel comprises ferrite.
- The rare earth-bearing heat-resistant alloy steel as claimed in claim 1 or 2, wherein the properties of the rare earth-bearing heat-resistant alloy steel satisfy at least one of: being able to withstand an applicable temperature of 1000-1300 °C; having an elongation of 5-25% and an oxidative weight loss of 0.2-8.0 g/(cm2•h) at the applicable temperature of 1000-1300 °C; and having an electrical resistivity of 1.3-1.5 µΩ•m at room temperature.
- A slab continuous casting production process for the rare earth-bearing heat-resistant alloy steel as claimed in any of claims 1 to 8, wherein in a continuous casting step, a specific water ratio of secondary cooling is controlled to be 1.02±0.10 L/kg.
- The slab continuous casting production process as claimed in claim 9, wherein in the continuous casting step, a temperature for hot grinding a casting slab is controlled to be 100-600 °C.
- The slab continuous casting production process as claimed in claim 9 or 10, wherein process parameters of the continuous casting step are controlled to satisfy at least one of:the specific water ratio of secondary cooling is controlled to be 1.02±0.06 L/kg;a temperature for hot grinding a casting slab is 300-500 °C;an electromagnetic stirring current is 1000-2000 A;a soft reduction amount is 3-10 mm;a solid fraction fs of casting slab center corresponding to a reduction zone is 0.10-0.90;a grinding amount on one casting slab side is 3-10 mm;a superheat degree of molten steel in a tundish is controlled to be 10-50 °C;an average casting speed of continuous casting is controlled to be 0.40-1.50 m/min; andan submerged depth of a continuous casting crystallizer nozzle is controlled to be 90-130 mm.
- The slab continuous casting production process as claimed in claim 11, wherein the process parameters of the continuous casting step are controlled to satisfy at least one of:the electromagnetic stirring current is 1400-2000 A;the soft reduction amount is 6-9 mm;the solid fraction fs of casting slab center corresponding to the reduction zone is 0.20-0.90;the grinding amount on one casting slab side is 5-8 mm;the superheat degree of molten steel in the tundish is controlled to be 15-30 °C;the average casting speed of continuous casting is controlled to be 0.80-1.2 m/min; andthe submerged depth insertion depth of the continuous casting crystallizer nozzle is controlled to be 100-125 mm.
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