TECHNICAL FIELD
[0001] 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.
BACKGROUND
[0002] 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.
[0003] 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.
[0004] 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.
SUMMARY
[0005] 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/(cm
2•h) at the applicable temperature of 1000-1300 °C, thus exhibiting good quality and
excellent heat resistance.
[0006] 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%.
[0007] 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%.
[0008] 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.
[0009] 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.
[0010] 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%.
[0011] In some preferred embodiments, the content of C in mass percentage can be controlled
to be 0.01≤C≤0.05%.
[0012] In some more preferred embodiments, the content of C in mass percentage can be controlled
to be 0.01≤C≤0.03%.
[0013] 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 Al
2O
3 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%.
[0014] In some preferred embodiments, the content of Si in mass percentage can be controlled
to be 0.02≤Si≤1.0%.
[0015] In some more preferred embodiments, the content of Si in mass percentage can be controlled
to be 0.2≤Si≤0.5%.
[0016] 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%.
[0017] In some preferred embodiments, the content of Mn in mass percentage can be controlled
to be 0.05≤Mn≤1.0%.
[0018] In some more preferred embodiments, the content of Mn in mass percentage can be controlled
to be 0.2≤Mn≤0.4%.
[0019] 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%.
[0020] In some preferred embodiments, the content of Cr in mass percentage can be controlled
to be 17.0-25.0%.
[0021] 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 Cr
2O
3 to Al
2O
3, 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%.
[0022] In some preferred embodiments, the content of Al in mass percentage can be controlled
to be 3.0-6.0%.
[0023] 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%.
[0024] In some preferred embodiments, the content of Nb in mass percentage can be controlled
to be 0<Nb≤0.40%.
[0025] In some more preferred embodiments, the content of Nb in mass percentage can be controlled
to be 0.02≤Nb≤0.40%.
[0026] In the most preferred embodiment, the content of Nb in mass percentage can be controlled
to be 0.05≤Nb≤0.40%.
[0027] 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%.
[0028] In some preferred embodiments, the content of Co in mass percentage can be controlled
to be 0<Co≤0.20%.
[0029] In some more preferred embodiments, the content of Co in mass percentage can be controlled
to be 0.01≤Co≤0.20%.
[0030] In the most preferred embodiment, the content of Co in mass percentage can be controlled
to be 0.05≤Nb≤0.20%.
[0031] 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%.
[0032] 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%.
[0033] 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%.
[0034] 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%.
[0035] 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.
[0036] 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%.
[0037] 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%.
[0038] 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 Al
2O
3 oxide film.
[0039] 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%.
[0040] Preferably, in the rare earth-bearing heat-resistant alloy steel of the present invention,
the main microstructure is ferrite.
[0041] 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/(cm
2•h) at the applicable temperature of 1000-1300 °C; and having an electrical resistivity
of 1.3-1.5 µΩ•m at room temperature.
[0042] 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.
[0043] 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.
[0044] 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.
[0045] 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.
[0046] 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.
[0047] 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.
[0048] 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.
[0049] 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.
[0050] 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.
[0051] 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.
[0052] 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.
[0053] 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.
[0054] 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.
[0055] 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.
[0056] 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/(cm
2•h) at the applicable temperature of 1000-1300 °C, exhibiting good quality and excellent
properties.
[0057] 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.
DETAILED DESCRIPTION
[0058] 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.
Inventive Examples 1-6 and Comparative Examples 1-4
[0059] 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 |
[0060] 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.
[0061] 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.
[0062] 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 |
[0063] 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".
[0064] 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 |
[0065] 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/(cm
2•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.
[0066] 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.
[0067] 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.
1. 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%.
2. 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.
3. 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%.
4. 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%.
5. 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%.
6. 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%.
7. 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.
8. 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.
9. 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.
10. 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.
11. 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;
and
an submerged depth of a continuous casting crystallizer nozzle is controlled to be
90-130 mm.
12. 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;
and
the submerged depth insertion depth of the continuous casting crystallizer nozzle
is controlled to be 100-125 mm.