CN112011730A - Slab continuous casting process for high-molybdenum high-chromium high-nitrogen steel and slab - Google Patents
Slab continuous casting process for high-molybdenum high-chromium high-nitrogen steel and slab Download PDFInfo
- Publication number
- CN112011730A CN112011730A CN201910456810.0A CN201910456810A CN112011730A CN 112011730 A CN112011730 A CN 112011730A CN 201910456810 A CN201910456810 A CN 201910456810A CN 112011730 A CN112011730 A CN 112011730A
- Authority
- CN
- China
- Prior art keywords
- slab
- molybdenum
- casting process
- chromium
- continuous casting
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- 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
- B22D11/108—Feeding additives, powders, or the like
-
- 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
-
- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- 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
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Continuous Casting (AREA)
- Treatment Of Steel In Its Molten State (AREA)
Abstract
The invention discloses a slab continuous casting process of high-molybdenum high-chromium high-nitrogen steel, which is characterized in that at least one of Al, B, Ca, Mg, Nb, Re, Ti, V and Zr is added into a crystallizer as a nucleating agent in the continuous casting process, and the addition amount of the nucleating agent is 0.001-0.5 wt%. In addition, the invention also discloses a high-molybdenum high-chromium high-nitrogen steel plate blank which is prepared by adopting the plate blank continuous casting process, wherein the high-molybdenum high-chromium high-nitrogen steel plate blank comprises 6-7 wt% of Mo, 20-22 wt% of Cr, 0.2-0.25 wt% of N, 24-26 wt% of Ni and 0.5-0.75 wt% of Cu. The slab obtained by the slab continuous casting process has good surface and center quality, is not easy to generate the phenomena of nitrogen segregation and precipitation, and has high production efficiency.
Description
Technical Field
The invention relates to a continuous casting process and a slab obtained by the same, in particular to a continuous casting process of high-nitrogen steel and a continuous casting slab thereof.
Background
The high-molybdenum high-chromium high-nitrogen steel contains elements such as molybdenum, chromium, nitrogen, copper and the like, wherein the mass percent of Mo is more than 6%, the mass percent of Cr is more than 20%, and the mass percent of N is more than 0.2%. With the rapid increase of market demand in recent years, the demand for the products is steadily improved, and particularly, the demand of the products is more vigorous than that of the products in the prior art due to the concern of China in the fields of petroleum and petrochemical industry, nuclear power and thermal power, clean energy, ship manufacturing, ocean engineering, environmental protection and the like. At present, only a small amount of test products of the Tai-Gao steel are put on the market in China, and basically all the Tai-Gao steel depends on import, mainly Japan metallurgy, and the Ottokupu and the American SMC are inferior. However, in the continuous casting and cooling process of the high-molybdenum high-chromium high-nitrogen steel, because of selective crystallization and element segregation and the precipitation of a mesophase in the solidification process, cracks are easy to generate.
Although there are techniques in the prior art that can achieve very fine grains and homogenize the structure, such as thermal control, vibration and chemical methods, they have some disadvantages, such as: the thermal control method is adopted to obtain fine crystals, a large amount of micro-porosity exists at the same time, and thermal isobaric treatment is needed to close shrinkage cavities and porosity; the use of the vibration method requires equipment to be updated, and both the thermal control method and the vibration method increase the production cost.
Therefore, a slab continuous casting process with high molybdenum, high chromium and high nitrogen is expected, the surface and the center of the slab obtained by the slab continuous casting process are good in quality, the phenomenon of nitrogen segregation and precipitation is not easy to occur, and the production efficiency is high.
Disclosure of Invention
The invention aims to provide a slab continuous casting process of high-molybdenum high-chromium high-nitrogen steel, and the slab obtained by the slab continuous casting process has good surface and center quality, is not easy to generate the phenomena of nitrogen segregation and precipitation and has high production efficiency.
In order to achieve the aim, the invention provides a slab continuous casting process of high-molybdenum high-chromium high-nitrogen steel, wherein at least one of Al, B, Ca, Mg, Nb, Re, Ti, V and Zr is added into a crystallizer as a nucleating agent in the continuous casting process, and the addition amount of the nucleating agent is 0.001-0.5 wt%.
In the slab continuous casting process according to the present invention, at least one of Al, B, Ca, Mg, Nb, Re, Ti, V, and Zr is added as a nucleating agent, whereby the generation of equiaxed crystals on the wall of the crystallizer can be promoted, the growth of primary crystals growing on the wall of the crystallizer can be suppressed at the root of the primary crystals, and the nucleation of crystal grains on the wall of the crystallizer can be promoted. Considering that if the amount of the nucleating agent is excessively added, the nucleation of crystal grains on the wall of the mold is excessively promoted, the stability of the solidified shell is lowered, and the cast slab is easily cracked, the amount of the nucleating agent added is controlled to be 0.001 to 0.5 wt% in the slab continuous casting process according to the present invention.
It should be noted that the addition of the nucleating agent may include feeding, dusting, particle or oxide metallurgy.
Furthermore, in the slab continuous casting process of the high-molybdenum high-chromium high-nitrogen steel, the addition amount of the nucleating agent is 0.002-0.25 wt%
Further, in the slab continuous casting process of the high-molybdenum high-chromium high-nitrogen steel, the induction heating power of the tundish is controlled to be 600-2000kW, and the superheat degree of the molten steel in the tundish is controlled to be 5-35 ℃.
In the scheme, the molten steel fluidity is poor if the superheat degree of the molten steel in the tundish is lower than 5 ℃, so that a crystallizer water port is easy to freeze steel, casting is forced to be interrupted, and the melting effect of the casting powder is poor; however, when the superheat degree of the molten steel in the tundish is higher than 35 ℃, for high-molybdenum high-chromium high-nitrogen steel, the solidification time is long, the selective crystallization is sufficient, the segregation and the looseness of a casting blank are aggravated, and the crack tendency is large. Based on the above, in the slab continuous casting process, the induction heating power of the tundish is controlled to be 600-2000kW, and the superheat degree of the molten steel in the tundish is controlled to be 5-35 ℃.
Furthermore, in the slab continuous casting process of the high-molybdenum high-chromium high-nitrogen steel, the induction heating power of the tundish is controlled to 800-1600kW, and the superheat degree of the molten steel in the tundish is controlled to 10-25 ℃.
Furthermore, in the slab continuous casting process of the high-molybdenum high-chromium high-nitrogen steel, the drawing speed is controlled to be 0.6-1.6 m/min.
In the scheme, the pulling speed is controlled to be 0.6-1.6m/min because: if the drawing speed is higher than 1.60m/min, the primary blank shell is thin, the casting blank is cooled unevenly, and longitudinal cracks and even steel leakage are easy to generate; however, if the pulling speed is lower than 0.60m/min, the casting blank is cooled in the crystallizer for too long time, molten steel at a meniscus is in a low-temperature state, the melting effect of the casting powder is poor, longitudinal cracking is easily caused, and the overall production capacity of a continuous casting machine is influenced. Therefore, in the slab continuous casting process, the drawing speed is controlled to be 0.6-1.6 m/min.
Furthermore, in the slab continuous casting process of the high-molybdenum high-chromium high-nitrogen steel, the drawing speed is controlled to be 0.6-1.2 m/min.
Further, in the slab continuous casting process of the high-molybdenum high-chromium high-nitrogen steel, the electromagnetic stirring current is 1000-2000A, and the stirring frequency is 2-5 Hz.
In the above scheme, in order to improve segregation and porosity which may be caused by high superheat of molten steel in the continuous casting process, it is preferable to add secondary cooling zone electromagnetic stirring in the slab continuous casting process of the present invention. Considering that if the electromagnetic stirring current intensity is lower than 1000A, the effect of improving the central quality of the casting blank cannot be achieved; and if the electromagnetic stirring current intensity is higher than 2000A, the liquid level fluctuation of the crystallizer is large, and the casting blank is easy to generate negative segregation. Based on the above, in the slab continuous casting process, the electromagnetic stirring current is controlled to be 1000-2000A, and the stirring frequency is 2-5 Hz.
Furthermore, in the slab continuous casting process of the high-molybdenum high-chromium high-nitrogen steel, the electromagnetic stirring current is 1200-1800A, and the stirring frequency is 2.5-3.5 Hz.
Furthermore, in the slab continuous casting process of the high-molybdenum high-chromium high-nitrogen steel, the reduction under dynamic light pressure is controlled to be 5-15 mm.
In the above-mentioned scheme, in order to improve segregation and porosity which may be caused by high superheat of molten steel in the continuous casting process, it is preferable to add a dynamic soft reduction process to the slab continuous casting process according to the present invention. Considering that if the reduction amount under the soft reduction is less than 5mm, the effect of improving the central quality of the casting blank cannot be achieved, and for high-molybdenum high-chromium high-nitrogen steel, the reduction amount under the dynamic soft reduction is more than 15mm, the narrow surface of the casting blank is easy to bulge, and cracks are easy to generate on the surface of the casting blank. Based on the above, in the slab continuous casting process, the reduction under dynamic light pressure is controlled to be 5-15 mm.
Accordingly, another object of the present invention is to provide a high-molybdenum high-chromium high-nitrogen slab which has good surface and center quality, is not prone to nitrogen segregation and precipitation, and has high production efficiency.
In order to achieve the aim, the invention also provides a high-molybdenum high-chromium high-nitrogen steel slab which is prepared by adopting the slab continuous casting process, wherein the high-molybdenum high-chromium high-nitrogen steel slab comprises 6-7 wt% of Mo, 20-22 wt% of Cr, 0.2-0.25 wt% of N, 24-26 wt% of Ni and 0.5-0.75 wt% of Cu.
Compared with the prior art, the slab continuous casting process of the high-molybdenum high-chromium high-nitrogen steel and the slab thereof have the following advantages and beneficial effects:
the slab continuous casting process of the high-molybdenum high-chromium high-nitrogen steel overcomes the defects of the prior art, the surface and the center of the slab obtained by the slab continuous casting process have good quality, the phenomena of nitrogen segregation and precipitation are not easy to occur, and the production efficiency is high.
In addition, the high-molybdenum high-chromium high-nitrogen steel slab disclosed by the invention also has the advantages and beneficial effects.
Detailed Description
The slab continuous casting process and the slab of the high molybdenum, high chromium and high nitrogen steel according to the present invention will be further explained and illustrated with reference to the specific examples, which, however, should not unduly limit the technical solution of the present invention.
The high molybdenum, high chromium and high nitrogen steels of examples 1-9 above were prepared by the following steps:
smelting and casting were carried out according to the chemical composition shown in Table 1, wherein the high-molybdenum, high-chromium, high-nitrogen steel slab had 6 to 7 wt% of Mo, 20 to 22 wt% of Cr, 0.2 to 0.25 wt% of N, 24 to 26 wt% of Ni, and 0.5 to 0.75 wt% of Cu, and at least one of Al, B, Ca, Mg, Nb, Re, Ti, V, and Zr was added as a nucleating agent in the crystallizer at the time of casting, and the amount of the nucleating agent added was 0.001 to 0.5 wt%. In addition, the power of the induction heating of the tundish is controlled to be 600-2000kW, the superheat degree of the molten steel in the tundish is controlled to be 5-35 ℃, the pulling speed is 0.6-1.6m/min, the electromagnetic stirring current is 1000-2000A, the stirring frequency is 2-5Hz, and the reduction under dynamic light pressure is 5-15 mm.
It should be noted that, in some preferred embodiments, the addition amount of the nucleating agent can be preferably controlled to be 0.002-0.25 wt%; the induction heating power of the tundish is 800-1600kW, and the superheat degree of the molten steel in the tundish is controlled at 10-25 ℃; the pulling speed is 0.6-1.2m/min, the electromagnetic stirring current is 1200-1800A, and the stirring frequency is 2.5-3.5 Hz.
In the above examples, the addition of the nucleating agent may include feeding, powder spraying, particle or oxide metallurgy.
Table 1 shows the mass percent of each chemical element of the high-molybdenum high-chromium high-nitrogen steel of examples 1-9.
TABLE 1 (wt%, balance Fe and unavoidable impurity elements other than P and S)
Table 2 lists the specific process parameters involved in the manufacture of the high molybdenum, high chromium, high nitrogen steels of examples 1-9.
Table 2.
Table 3 shows the slab quality of examples 1 to 9 in this case
Table 3.
| Examples | Quality of casting blank |
| 1 | No crack, central porosity and segregation of grade 1.5 |
| 2 | No crack, central porosity and segregation of grade 1.0 |
| 3 | No crack, central porosity and segregation of 0.5 grade |
| 4 | No crack, central porosity and segregation of grade 1.5 |
| 5 | No crack, central porosity and segregation of grade 1.0 |
| 6 | No crack, central porosity and segregation of 0.5 grade |
| 7 | No crack, central porosity and segregation of 0.5 grade |
| 8 | The material has no crack and the like,central porosity and segregation of 0.5 grade |
| 9 | No crack, central porosity and segregation of grade 1.0 |
As can be seen from table 3, the high-molybdenum, high-chromium and high-nitrogen steel finally obtained by the slab continuous casting process can well overcome the defects of the prior art, the surface and center quality of each embodiment is good, the phenomena of nitrogen segregation and precipitation are not easy to occur, and the production efficiency is high.
In conclusion, the slab continuous casting process for the high-molybdenum high-chromium high-nitrogen steel overcomes the defects in the prior art, the surface and the center of the slab obtained by the slab continuous casting process are high in quality, the phenomena of nitrogen segregation and precipitation are not easy to occur, and the production efficiency is high.
In addition, the high-molybdenum high-chromium high-nitrogen steel slab disclosed by the invention also has the advantages and beneficial effects.
It should be noted that the prior art in the protection scope of the present invention is not limited to the examples given in the present application, and all the prior art which is not inconsistent with the technical scheme of the present invention, including but not limited to the prior patent documents, the prior publications and the like, can be included in the protection scope of the present invention.
In addition, the combination of the features in the present application is not limited to the combination described in the claims of the present application or the combination described in the embodiments, and all the features described in the present application may be freely combined or combined in any manner unless contradictory to each other.
It should also be noted that the above-mentioned embodiments are only specific examples of the present invention, and it is obvious that the present invention is not limited to the above-mentioned embodiments, and many similar variations are possible. All modifications which would occur to one skilled in the art and which are, therefore, directly derived or suggested from the disclosure herein are deemed to be within the scope of the present invention.
Claims (10)
1. A slab continuous casting process of high-molybdenum high-chromium high-nitrogen steel is characterized in that at least one of Al, B, Ca, Mg, Nb, Re, Ti, V and Zr is added into a crystallizer as a nucleating agent in the continuous casting process, and the addition amount of the nucleating agent is 0.001-0.5 wt%.
2. The process for slab casting of high molybdenum, high chromium, and high nitrogen steel as claimed in claim 1, wherein the amount of nucleating agent added is 0.002 to 0.25 wt%.
3. The slab continuous casting process of high molybdenum high chromium high nitrogen steel as claimed in claim 1 or 2, characterized in that the induction heating power of the tundish is controlled to 600-2000kW, and the superheat degree of the molten steel in the tundish is controlled to 5-35 ℃.
4. The slab continuous casting process of high molybdenum high chromium high nitrogen steel as claimed in claim 3, characterized in that the induction heating power of the tundish is controlled to 800-.
5. The slab casting process of high molybdenum, high chromium and high nitrogen steel as claimed in claim 1 or 2, characterized in that the casting speed is controlled to 0.6-1.6 m/min.
6. The slab casting process of high molybdenum, high chromium and high nitrogen steel as claimed in claim 5, wherein the casting speed is controlled to 0.6-1.2 m/min.
7. The slab continuous casting process of high molybdenum high chromium high nitrogen steel as claimed in claim 1 or 2, characterized in that the electromagnetic stirring current is 1000-2000A and the stirring frequency is 2-5 Hz.
8. The continuous slab casting process of high molybdenum, high chromium and high nitrogen steel as claimed in claim 7, wherein the electromagnetic stirring current is 1200-1800A, and the stirring frequency is 2.5-3.5 Hz.
9. The slab casting process of high molybdenum, high chromium and high nitrogen steel as claimed in claim 1, wherein the reduction under dynamic light pressure is controlled to be 5-15 mm.
10. A high molybdenum high chromium high nitrogen steel slab produced by the slab continuous casting process according to any one of claims 1 to 9, wherein Mo is 6 to 7 wt%, Cr is 20 to 22 wt%, N is 0.2 to 0.25 wt%, Ni is 24 to 26 wt%, and Cu is 0.5 to 0.75 wt% in the high molybdenum high chromium high nitrogen steel slab.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201910456810.0A CN112011730B (en) | 2019-05-29 | 2019-05-29 | Slab continuous casting process for high-molybdenum high-chromium high-nitrogen steel and slab |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201910456810.0A CN112011730B (en) | 2019-05-29 | 2019-05-29 | Slab continuous casting process for high-molybdenum high-chromium high-nitrogen steel and slab |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN112011730A true CN112011730A (en) | 2020-12-01 |
| CN112011730B CN112011730B (en) | 2022-03-18 |
Family
ID=73500811
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201910456810.0A Active CN112011730B (en) | 2019-05-29 | 2019-05-29 | Slab continuous casting process for high-molybdenum high-chromium high-nitrogen steel and slab |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN112011730B (en) |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1743491A (en) * | 2004-08-30 | 2006-03-08 | 宝山钢铁股份有限公司 | Manufacture method for obtaining superfine crystal grain steel |
| CN101812647A (en) * | 2009-02-25 | 2010-08-25 | 宝山钢铁股份有限公司 | Diphase stainless steel and manufacturing method thereof |
| CN102776322A (en) * | 2012-08-03 | 2012-11-14 | 北京科技大学 | Method for treating impurities in pipe line steel by adopting nucleant refined crystal grains |
| CN105543711A (en) * | 2015-12-22 | 2016-05-04 | 东北大学 | Cast-rolling method for restraining Cr element and Mo element of super-austenitic stainless steel from center segregation |
-
2019
- 2019-05-29 CN CN201910456810.0A patent/CN112011730B/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1743491A (en) * | 2004-08-30 | 2006-03-08 | 宝山钢铁股份有限公司 | Manufacture method for obtaining superfine crystal grain steel |
| CN101812647A (en) * | 2009-02-25 | 2010-08-25 | 宝山钢铁股份有限公司 | Diphase stainless steel and manufacturing method thereof |
| CN102776322A (en) * | 2012-08-03 | 2012-11-14 | 北京科技大学 | Method for treating impurities in pipe line steel by adopting nucleant refined crystal grains |
| CN105543711A (en) * | 2015-12-22 | 2016-05-04 | 东北大学 | Cast-rolling method for restraining Cr element and Mo element of super-austenitic stainless steel from center segregation |
Non-Patent Citations (5)
| Title |
|---|
| 孙立根: "《连铸设计原理》", 31 August 2017 * |
| 朱苗勇等: "《现代冶金工艺学 钢铁冶金卷》", 31 December 2016 * |
| 王亚男等: "《材料科学基础教程》", 31 August 2011 * |
| 王家新: "《金属的凝固及其控制》", 30 June 1983 * |
| 蔡开科: "《连铸坯质量控制》", 31 May 2010 * |
Also Published As
| Publication number | Publication date |
|---|---|
| CN112011730B (en) | 2022-03-18 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN108546834B (en) | Purification smelting method for nickel-based high-temperature alloy master alloy | |
| CN102828103B (en) | Alloy gray cast iron glass mould and method for producing same | |
| CN104894466A (en) | High-strength, high-elasticity modulus and low-stress gray cast iron and manufacturing method thereof | |
| CN105568122B (en) | φ 280mm 30CrMo circular pipe blank center segregation control methods | |
| CN102925783A (en) | Method for preparing hypereutectic high chromium white cast iron | |
| CN103866192A (en) | Low-resistivity steel and manufacturing method thereof | |
| CN115094263B (en) | Alterant alloy for copper-chromium-zirconium series alloy, preparation method and application thereof | |
| CN115710654A (en) | Copper-nickel-tin alloy and preparation method thereof | |
| CN105803149A (en) | Equiaxial crystal ratio control method for 35CrMo round pipe billet with phi 280 mm | |
| CN112011730B (en) | Slab continuous casting process for high-molybdenum high-chromium high-nitrogen steel and slab | |
| CN102517476B (en) | High strength aluminum alloy capable of reducing porosity and dispersed shrinkage and preparation method thereof | |
| CN101979186A (en) | Method for controlling graphite distortion of large-sized nodular iron casting | |
| CN108380835B (en) | Low-segregation gas valve steel continuous casting billet and manufacturing method thereof | |
| CN114657428A (en) | Processing technology and preparation method of improved refrigerator foaming die casting | |
| CN107419201A (en) | A kind of amorphous alloy material production method of high saturated magnetic induction | |
| CN105603300A (en) | Center segregation control method of phi280mm 35CrMo circular tube blank | |
| CN110157975B (en) | Preparation method of high-strength thin-wall gray iron casting | |
| CN112011747A (en) | High-nitrogen steel and slab continuous casting process thereof | |
| CN113265595B (en) | Continuous casting billet for low-alloy seamless tube and production method thereof | |
| CN103233170A (en) | Steel for hot working mold and production method thereof | |
| CN109365525B (en) | Method for controlling quality of cold-rolled silicon steel casting blank | |
| CN105695658A (en) | Method for controlling equiaxial crystal ratio of phi-280mm 30CrMo circular tube blank | |
| JP3658488B2 (en) | Method for producing eutectic graphite cast iron | |
| CN112517862B (en) | Secondary hole shrinkage control method for large-size high-temperature alloy master alloy cast ingot | |
| CN108085537A (en) | The copper alloy glass mold production method of control molding facial disfigurement |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |