CN1704495A - A method for enduing high-vanadium high-cobalt high-speed steel with superplasticity property - Google Patents
A method for enduing high-vanadium high-cobalt high-speed steel with superplasticity property Download PDFInfo
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- 229910000997 High-speed steel Inorganic materials 0.000 title claims abstract description 52
- 238000000034 method Methods 0.000 title claims abstract description 43
- 229910017052 cobalt Inorganic materials 0.000 title claims abstract description 37
- 239000010941 cobalt Substances 0.000 title claims abstract description 37
- 229910052720 vanadium Inorganic materials 0.000 title claims abstract description 37
- 238000001816 cooling Methods 0.000 claims abstract description 21
- 239000000956 alloy Substances 0.000 claims abstract description 19
- 238000005098 hot rolling Methods 0.000 claims abstract description 19
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims abstract description 5
- 238000005507 spraying Methods 0.000 claims abstract description 5
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims abstract description 5
- 238000010438 heat treatment Methods 0.000 claims description 19
- 238000009718 spray deposition Methods 0.000 claims description 16
- 238000005096 rolling process Methods 0.000 claims description 14
- 239000000155 melt Substances 0.000 claims description 9
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 8
- 239000007788 liquid Substances 0.000 claims description 5
- 230000008018 melting Effects 0.000 claims description 5
- 238000002844 melting Methods 0.000 claims description 5
- 239000000758 substrate Substances 0.000 claims description 5
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 4
- 238000000151 deposition Methods 0.000 claims description 4
- 239000011261 inert gas Substances 0.000 claims description 4
- 229910052757 nitrogen Inorganic materials 0.000 claims description 4
- 230000006698 induction Effects 0.000 claims description 3
- 238000004321 preservation Methods 0.000 claims description 3
- 229910052786 argon Inorganic materials 0.000 claims description 2
- 239000000126 substance Substances 0.000 claims description 2
- 229910045601 alloy Inorganic materials 0.000 abstract description 10
- 238000005516 engineering process Methods 0.000 abstract description 2
- 239000000463 material Substances 0.000 description 31
- 229910000831 Steel Inorganic materials 0.000 description 10
- 239000010959 steel Substances 0.000 description 10
- 238000000137 annealing Methods 0.000 description 6
- 238000005520 cutting process Methods 0.000 description 6
- 238000010791 quenching Methods 0.000 description 6
- 230000000171 quenching effect Effects 0.000 description 6
- 150000001247 metal acetylides Chemical class 0.000 description 5
- 238000004663 powder metallurgy Methods 0.000 description 4
- 238000003466 welding Methods 0.000 description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 3
- 230000008901 benefit Effects 0.000 description 3
- 230000005496 eutectics Effects 0.000 description 3
- 238000005242 forging Methods 0.000 description 3
- 229910001349 ledeburite Inorganic materials 0.000 description 3
- 239000000843 powder Substances 0.000 description 3
- 239000002436 steel type Substances 0.000 description 3
- 230000035882 stress Effects 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- CPLXHLVBOLITMK-UHFFFAOYSA-N Magnesium oxide Chemical compound [Mg]=O CPLXHLVBOLITMK-UHFFFAOYSA-N 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
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- 238000001746 injection moulding Methods 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 238000003825 pressing Methods 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- 238000005496 tempering Methods 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910001311 M2 high speed steel Inorganic materials 0.000 description 1
- 229910001315 Tool steel Inorganic materials 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 238000000280 densification Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000001513 hot isostatic pressing Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 239000000395 magnesium oxide Substances 0.000 description 1
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- 239000011148 porous material Substances 0.000 description 1
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- 230000035945 sensitivity Effects 0.000 description 1
- 238000005245 sintering Methods 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
- 230000008646 thermal stress Effects 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 239000002699 waste material Substances 0.000 description 1
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Abstract
Disclosed is a method for enduing high-vanadium high-cobalt high-speed steel with superplasticity property which comprises the following steps, selecting master alloys, obtaining high speed steel block body with high vanadium and cobalt content with spraying forming technology, carrying out hot-rolling at a temperature of 950-1100 deg. C, keeping the reduction in pass to be 50-80%, and controlling the cooling down process. The invention can realize the one-time forming for knife tools and die arrangements with rather complex shapes.
Description
Technical Field
The invention relates to a process method for obtaining superplasticity of high-vanadium high-cobalt high-speed steel.
Background
The high-vanadium high-cobalt high-speed steel is high-carbon high-alloy ledeburite steel, and is not only widely used for high-speed, large-feed-rate and high-depth cutting, but also used for cutting high-hardness, high-toughness and other materials difficult to process. However, the types of the alloy elements added in the steel are more, and the content is quite high, so the high-vanadium high-cobalt high-speed steel belongs to the alloy steel type which is difficult to machine and form.
At present, people carry out extensive research on the superplasticity of materials in order to solve the problems of difficult processing and difficult forming of the materials. The material has superplastic properties when it exhibits, when stretched under conditions of temperature and rate of deformation, the properties of large elongation (over 100%) and small resistance to deformation. When the material is in a superplasticstate, the forming processing of the metal has the following advantages:
high plasticity and low strength, and the forming load is lower than that of common plastic materials, thus greatly saving energy, saving processing cost and reducing material loss.
The load used by superplastic forming is small, the speed is low, so the requirement on the strength of the die is not high, and the die is not easy to damage when in use.
The metal material has low strength and extremely high plasticity in a superplastic state, has low resistance to fracture, and is easy to be cut or machined.
For the tool and the die with complex shapes, the waste of materials and working hours can be caused by using the conventional cutting processing, and if the superplastic forming technology is adopted, not only the tool and the die with complex shapes can be formed at one time, but also higher precision and low surface roughness can be obtained.
For the high-vanadium high-cobalt high-speed steel added with expensive alloy elements, if the high-vanadium high-cobalt high-speed steel has superplasticity, not only can a cutter and a die with complex shapes be formed at one time, but also the high-speed steel can be connected with other steel types through friction welding or diffusion welding, and the high-vanadium high-cobalt high-speed steel has great economic significance and practical value.
There are many ways of imparting superplasticity to materials today. Among them, a method of how to ultrafinely, equiaxially and stably crystallize material grains is a main aspect. Because the grain boundary area in the ultra-fine grain alloy is large, the grain boundary plasticity is good at high temperature, and viscous flow can be carried out, so that the material has superplasticity at high temperature.For high speed steel, the current technological means for superplasticizing high speed steel are successful powder metallurgy methods, Г a г a etc. (К a Г a г a, et al "c t h у к b у P h a г c e r P h r P3 g h a3 a3 a b h a3 a b l3 b h a3 b h b Бы c h a r a3 a P h a3 b z h a3 b z h a b 4 a b z h a b г b 460 b у г b х c a b 9 b h a b 9 b a b 9 b-4s-1The super-plasticity of the alloy has good super-plasticity at a strain rate, and the elongation rate of the alloy can reach up to 630 percent. The powder metallurgy process comprises the following steps: powder low-temperature pressing → sintering → high-temperature pressing → annealing. Yasunori Torsaka et al (Yasunori Torsaka, Ichiro Uui, Yoshiori Nakazawa, Matsuo Miyagawa, "High-speed Tool Steel cutting Recristallized Hyperfine steels and Italic". Tetsu-to-Haganone 1985, vol 71: 735-742, Japan) in Japan use a recrystallization process to make KHA30 powdered High speed Steel have a tensile strain rate of 2.5X 10 at a temperature of 1000 deg.C-4s-1① forging or rolling powder high speed steel KHA30 at 950 ℃ for 5% and water cooling, water quenching after preserving heat at ② 1150 ℃ for 5 minutes, preserving heat at ③ 700 ℃ for 1 hour and annealing, but the powder metallurgy process for obtaining the powder metallurgy high speed steel KHA30 is quite complex, and the steps comprise atomized powder with the particle size of below 250 mu m → 1100 ℃, 800atm hot isostatic pressing at 800atm temperature → furnace cooling → forging at 1100 ℃ (forging ratio of 6) → annealing, wherein the annealing process is:
from their above-mentioned processes, it can be seen that the whole process from the preparation of high-speed steel to its superplastic properties is rather complicated and costly, requiring expensive investments in equipment. Other processes for imparting superplastic properties to high speed steels are heat treatment processes.
The Wangmin is processed by a circulating quenching method (Wangmin, Chenshihong and Geliling, the influence of circulating heat treatment on the superplasticity of high-speed steel is shown in the metal forming process, vol14, No.6, 1996: P16-18, the mechanical behavior of tissue ultra-fining and superplasticity deformation of high-speed steel, steel and iron, vol33, No.9, 1998: P49-51), so that the W6Mo5Cr4V2(M2) high-speed steel has the initial strain rate of 3.33 multiplied by 10 at the temperature of 810℃ and the initial strain rate of 3.33 multiplied by 10-4s-1192% high temperature tensile elongation is obtained at optimum deformation conditions with a maximum rheological stress of 58 MPa. The specific heat treatment process scheme is 1040 ℃ multiplied by 3min oil quenching, 850 ℃ multiplied by 1h annealing, 1040 ℃ multiplied by 3min oil quenching and 550 ℃ multiplied by 2h annealing. Trekko 2233131, et al (trekko 2233131Relation of superplasticity of high speed steel. vol.28, No.7, 1993: 45-50.) through quenching and tempering, the M2 high-speed steel is subjected to quenching and tempering treatment at 800 ℃ and the initial strain rate of 8.33 multiplied by 10-4s-1At 210% high temperature tensile elongation, and Г у я E (Г у я, A. П. C.E E х п Pi a b E a T E ч B P E B A H E H E T E7H G E B A H E B A, M A3E B, M A у P г E я, 1982, 18.) similar results were obtained with heat treatmentc1So high temperature tensile elongation occurs near the temperature point. Moreover, the range of superplastic deformation temperatures (about 50 ℃) and the range of deformation speeds are rather narrow, with the result that the precision requirements on the temperature control devices and the forming devices during testing or production are so high that this property of the material cannot be fully exploited.
Disclosure of Invention
The invention aims to provide a method for obtaining superplasticity performance of high-vanadium high-cobalt high-speed steel, which adopts a simple process and has lower cost; moreover, the superplasticity of the material is more excellent.
In order to achieve the purpose, the technical scheme of the invention is as follows:
a method for obtaining superplasticity of high-vanadium high-cobalt high-speed steel is characterized by comprising the following steps:
a. selecting a proper high-vanadium high-cobalt high-speed steel master alloy material, wherein the chemical components (wt%) of the master alloy material are as follows:
1.1-2.18% of C, 5.0-7.0% of W, 4.0-6.0% of Mo4, 3.0-5.0% of Cr3, 2.2-8.3% of V, 6.5-9.5% of Co6, and the balance of Fe;
b. adopting a spray forming process to obtain a high-vanadium high-cobalt high-speed steel block;
c. then, a large-reduction hot rolling method is adopted, the hot rolling heating temperature is selected to be 950-1100 ℃, the hot rolling heating heat preservation time follows that t is d x (1.0-2.0) min/mm (d is the thickness of a rolling sample), and the reduction of each pass is 50-80%;
d. and cooling after hot rolling, wherein the cooling speed is controlled to be 1-10 ℃/min.
Wherein, the spray forming process comprises the following steps:
i. putting the high-vanadium high-cobalt high-speed steel master alloy material into an induction furnace for heating to melt the master alloy material;
ii, keeping for a period of time at the temperature of 100-250 ℃ higher than the melting point to ensure that the temperature and the components of the melt are uniform;
and iii, spraying high-pressure inert gas to the melt to atomize the melt into fine liquid drops, flying and depositing the fine liquid drops on a collecting substrate, cooling and solidifying to form a block.
In the spray forming process, the inert gas is nitrogen or argon.
The superplastic high-temperature tensile deformation temperature range of the high-vanadium high-cobalt high-speed steel is 780-1100 ℃; strain rate at deformation in the range of 1.0X 10-4s-1～1.0×10-1s-1。
1. The spray forming process is used for obtaining uniform equiaxial fine grain structure of the high-vanadium high-cobalt high-speed steel through spray forming. Because the solidification cooling speed is high, continuous network carbide does not appear in the structure, only discontinuously distributed fine carbide exists, and segregation is avoided. However, since the high-speed steel particles and droplets impact the substrate during the spray forming process, the temperature of the billet is increased while the billet is deposited. If the degree of superheat is high, network carbides and eutectic ledeburitics that affect material properties may be present in the unsolidified droplets present during deposition. Therefore, for high-vanadium high-cobalt high-speed steel, the principle of low-temperature fast casting should be followed. The degree of superheat of the injection molding cannot be too low, however, because if it is too low, the number of pores in the deposited blank increases. In summary, controlling the degree of superheat of molten steel is one of the key factors in the injection molding process. The superheat degree adopted by the invention is 100-250 ℃ higher than the melting point temperature of steel.
2. Hot rolling process under large pressure. By this hot rolling process, two objectives can be achieved: on one hand, the spray forming blank of the high-vanadium high-cobalt high-speed steel can be densified, and the density is close to the theoretical density. Although spray forming makes the steel free from segregation and uniform and fine in structure, the material itself obtained by the spray forming process is not completely dense, and besides a certain number of holes, there are a relatively large number of carbides having a relatively high hardness such as MC type carbides, which have a strong sensitivity to the holes existing in the steel, and thus the high-temperature tensile elongation of the material may not be high. It is therefore necessary to achieve densification of the material. On the other hand, since large-sized droplets inevitably occur during atomization in spray forming, the large droplets cause network carbides and eutectic ledeburite during deposition because the cooling rate is somewhat slow. The presence of these network carbides and eutectic ledeburite can affect the properties of the material and must be removed or comminuted using hot working. To achieve these two objectives, the temperature and reduction of the hot rolling must be strictly controlled. For high-vanadium high-cobalt high-speed steel, the heating speed, heating temperature and holding time of hot rolling need to be controlled, and if the heating speed is too high, thermal stress is easily generated in the steel. If the heating temperature is too high, the carbide is significantly coarsened and horned, and cracks are easily generated in the subsequent rolling process. Too long a holding time will also cause the growth of grains. The rolling heating speed used by the invention is controlled within the range of 1-10 ℃/min, the rolling heating temperature is 950-1100 ℃, and the heat preservation time follows that t is d multiplied by 1.0-2.0 min/mm (d is the thickness of a rolling sample). Theinitial rolling temperature is 950-1000 ℃. The finishing temperature is controlled to be 850-900 ℃. In order to enable the material to be compact, the reduction per pass is controlled to be 50-80%.
3. Cooling the rolled material. How to cool the material to room temperature after rolling is also a critical issue. If the air cooling or faster cooling mode is adopted, because the alloy content and the carbon content of the high-vanadium high-cobalt high-speed steel are high, the phase transformation from austenite to martensite can occur, twin martensite is formed, and cracks are initiated along with the generation of internal stress. Cracks initiated during subsequent room temperature storage can easily propagate, resulting in material scrap. When furnace cooling is carried out at a certain temperature, part of carbide grows while stress is removed, and finally the performance of the material is deteriorated. And therefore a suitable cooling means is required. The cooling speed of the rolled material is controlled within the range of 1-10 ℃/min, so that the cooling is prevented from being too fast, and the growth of carbide in the material is also prevented.
The invention has the advantages of
The high-vanadium high-cobalt high-speed steel obtained by adopting the spray forming process and combining the high-reduction hot rolling is 1.0 multiplied by 10-4s-1～1.0×10-2s-1The strain rate of the high-temperature-resistant steel has a high-temperature tensile elongation of up to 327% at 780-1000 ℃; meanwhile, the superplastic deformation temperature is quite wide, and the high tensile elongation is realized at the temperature from 780 ℃ to 1000 ℃ or even higher. At a relatively high strain rate (1.0X 10)-1s-1Near the level of conventional processing means) the material may still have more than 100% high temperature tensile elongation at certain temperature points. Benefit toThe invention makes the high-vanadium high-cobalt high-speed steel added with expensive alloy elements obtain superplasticity, can realize the one-step forming of cutters and molds with more complex shapes, greatly reduces the consumption of materials, energy and time, can realize the connection of the high-vanadium high-cobalt high-speed steel and other steel types through friction welding or diffusion welding, and has great economic significance and practical value.
Detailed Description
The high-vanadium high-cobalt high-speed steel master alloy adopted by the invention comprises the following components in percentage by weight: c1.31, W5.11, Mo4.16, Cr4.33, V3.12, Co6.64, Si0.06, Mn0.19, P0.022 and S0.011.
Spray forming, wherein the spray forming operation process comprises the following steps: putting the high-speed steel master alloy material (casting bar) into an induction furnace for heating and melting; keeping for a period of time at a temperature about 150 ℃ higher than the melting point to make the temperature and the components of the melt uniform; then high-pressure nitrogen is sprayed to the melt, so that the melt is atomized into fine droplets, flies and is deposited on a collecting substrate to finish solidification and form a block. The diameter of the liquid guide tube used in the spraying process is 4.5mm, the pressure of atomized nitrogen is 2.5MPa, the spraying distance is 350mm, the rotating speed of the substrate is 10rpm, and the gas/melt flow ratio (G/M) is about 0.40M3/kg。
Hot rolling, preparing a strip sample with the width of 21mm, the thickness of 20mm and the length of 85mm from the spray-formed blank by linear cutting, and making the front end into a wedge shape so as to bite in the rolling process.
Putting the sample into a box-type resistance furnace, heating the sample from 500 ℃ to 1020 ℃ along with the furnace at the heating speed of 2 ℃/min, and preserving the heat for 20 minutes; immediately after the sample is taken out, the sample is sent to a hot rolling mill with the maximum rolling force of 3000kN for rolling. The temperature of the sample is reduced by 40-80 ℃ from the sample taking out to the rolling (measured by an infrared temperature tester). The diameter of the roller of the rolling mill is 370mm, and the rotating speed is 20 r/min. The sample is rolled from 20mm thick to 6mm thick in one pass at a reduction of 70%.
And cooling after hot rolling, putting the high-vanadium high-cobalt high-speed steel sample into magnesia preheated at the temperature of about 400 ℃ after hot rolling, and cooling along with the sand at the cooling speed of about 3.8 ℃/min. The density of the material measured by a drainage method taking Archimedes' law as a principle is as follows: 8.0585g/cm3Close to the theoretical density.
Superplasticity test
And sampling the hot rolled sample by adopting a linear cutting method to prepare a tensile sample with a certain size. Performing high-temperature superplastic stretching within the temperature range of 780-1000 ℃. The stretching results are shown in table 1.
The results show that:
after the steps, the high-vanadium high-cobalt high-speed steel is 2.5 multiplied by 10-4s-1Or 5.0X 10-3s-1Has a tensile elongation at elevated temperature of up to 327%.
The superplastic deformation temperature is quite wide, and the temperature from 780 ℃ to 950 ℃ or even higher has relatively high tensile elongation. Therefore, the precision requirements on temperature control equipment and forming equipment in the test or production process are reduced, and the superplasticity of the material can be fully utilized.
At a relatively high strain rate (1.0X 10)-1s-1Near the level of conventional processing means) the material may still have more than 100% high temperature tensile elongation at certain temperature points. This has not been similarly reported for high speed steels.
Therefore, the superplasticity of the high-vanadium high-cobalt high-speed steel obtained by the method can directly form a tool piece, greatly reduces the consumption of materials, energy and time, and has important economic value undoubtedly. Table 1 shows the results of high temperature superplastic drawing of high vanadium and cobalt high speed steel after spray forming and hot rolling at high reduction.
TABLE 1
Claims (4)
1. A method for obtaining superplasticity of high-vanadium high-cobalt high-speed steel is characterized by comprising the following steps:
a. selecting a proper high-vanadium high-cobalt high-speed steel master alloy material, wherein the chemical components (wt%) of the master alloy material are as follows:
1.1-2.18% of C, 5.0-7.0% of W, 4.0-6.0% of Mo4, 3.0-5.0% of Cr3, 2.2-8.3% of V, 6.5-9.5% of Co6, and the balance of Fe;
b. adopting a spray forming process to obtain a high-vanadium high-cobalt high-speed steel block;
c. then, a large-reduction hot rolling method is adopted, the hot rolling heating temperature is selected to be 950-1100 ℃, the hot rolling heating heat preservation time follows that t is d x (1.0-2.0) min/mm (d is the thickness of a rolling sample), and the reduction of each pass is 50-80%;
d. and cooling after hot rolling, wherein the cooling speed is controlled to be 1-10 ℃/min.
2. The method for obtaining superplasticity of high vanadium high cobalt high speed steel according to claim 1, wherein: the spray forming process comprises the following steps:
i. putting the high-vanadium high-cobalt high-speed steel master alloy material into an induction furnace for heating to melt the master alloy material;
ii, keeping for a period of time at the temperature of 100-250 ℃ higher than the melting point to ensure that the temperature and the components of the melt are uniform;
and iii, spraying high-pressure inert gas to the melt to atomize the melt into fine liquid drops, flying and depositing the fine liquid drops on a collecting substrate, cooling and solidifying to form a block.
3. The method for obtaining superplasticity of high vanadium high cobalt high speed steel according to claim 2, characterized in that: the inert gas is nitrogen or argon.
4. The method for obtaining superplasticity of high vanadium high cobalt high speed steel according to claim 1, wherein: the superplastic high-temperature tensile deformation temperature range of the high-vanadium high-cobalt high-speed steel is 780-1100 ℃; strain rate at deformation in the range of 1.0X 10-4s-1～1.0×10-1s-1。
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101559490B (en) * | 2009-04-17 | 2011-01-05 | 中国航空工业第一集团公司北京航空材料研究院 | Method for preparing double-scanning and spray forming high-speed steel under purification |
| CN104175065A (en) * | 2014-06-30 | 2014-12-03 | 贵州安大航空锻造有限责任公司 | Superplastic forming method of 1Cr21Ni5Ti duplex stainless steel complex section ring piece |
| WO2016184007A1 (en) * | 2015-05-15 | 2016-11-24 | 河冶科技股份有限公司 | Spray formed high-speed steel |
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| RU2069602C1 (en) * | 1991-12-25 | 1996-11-27 | Акционерное общество "Тико Инвест" | Method to produce pieces of powder quick-cutting steel |
| CN1159470C (en) * | 2001-09-30 | 2004-07-28 | 宝山钢铁股份有限公司 | Ultrahigh carbon steel base material with superplasticity, its production method and application |
| RU2219255C1 (en) * | 2002-08-09 | 2003-12-20 | Тульский государственный университет | Method of working high-speed steel |
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101559490B (en) * | 2009-04-17 | 2011-01-05 | 中国航空工业第一集团公司北京航空材料研究院 | Method for preparing double-scanning and spray forming high-speed steel under purification |
| CN104175065A (en) * | 2014-06-30 | 2014-12-03 | 贵州安大航空锻造有限责任公司 | Superplastic forming method of 1Cr21Ni5Ti duplex stainless steel complex section ring piece |
| CN104175065B (en) * | 2014-06-30 | 2016-08-24 | 贵州安大航空锻造有限责任公司 | The super plastic forming method of 1Cr21Ni5Ti two phase stainless steel complex section annular element |
| WO2016184007A1 (en) * | 2015-05-15 | 2016-11-24 | 河冶科技股份有限公司 | Spray formed high-speed steel |
| US10233519B2 (en) | 2015-05-15 | 2019-03-19 | Heye Special Steel Co., Ltd. | Spray-formed high-speed steel |
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| CN100340678C (en) | 2007-10-03 |
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