[go: up one dir, main page]

WO2016011759A1 - Procédé de forgeage pour noyau mou à ultra-haute température d'un lingot d'acier - Google Patents

Procédé de forgeage pour noyau mou à ultra-haute température d'un lingot d'acier Download PDF

Info

Publication number
WO2016011759A1
WO2016011759A1 PCT/CN2014/092623 CN2014092623W WO2016011759A1 WO 2016011759 A1 WO2016011759 A1 WO 2016011759A1 CN 2014092623 W CN2014092623 W CN 2014092623W WO 2016011759 A1 WO2016011759 A1 WO 2016011759A1
Authority
WO
WIPO (PCT)
Prior art keywords
forging
steel ingot
ingot
high temperature
ultra
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.)
Ceased
Application number
PCT/CN2014/092623
Other languages
English (en)
Chinese (zh)
Inventor
李殿中
孙明月
栾义坤
刘宏伟
傅排先
徐斌
李依依
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Institute of Metal Research of CAS
Original Assignee
Institute of Metal Research of CAS
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Institute of Metal Research of CAS filed Critical Institute of Metal Research of CAS
Publication of WO2016011759A1 publication Critical patent/WO2016011759A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

Links

Images

Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor

Definitions

  • the present invention relates to the field of forging of steel, and more particularly to an ultra-high temperature soft core forging method for a die cast steel ingot.
  • the size and distribution of central defects are difficult to quantify by uniform standards.
  • Different ingot types are used for the same forging process, and some can pass the inspection.
  • the 42CrMo and H13 steel ingots are produced using a 15 ton ingot with a height to diameter ratio of 2, and the forging is also applied by the WHF method.
  • the forged piece of 42CrMo material can pass the flaw detection, but the H13 cannot pass, mainly because the H13 solidification interval is wide and the shrinkage hole is small. Loose defects are more serious. This status quo indicates that the current center compaction process is not sufficient to eliminate some of the more serious defects in the steel ingot center. Therefore, it is imperative to develop a more powerful and effective forging method and completely eliminate the defects in the center of the steel ingot.
  • Method 1 For some steel ingots with lower weight, the steel ingot is first poured, the ingot is cooled to 300-500 ° C in the ingot mold, and then to avoid cracking when it is cooled to room temperature, long-term stress relief annealing is required, and then Long-term gradient reheating in the furnace, the temperature inside and outside the steel ingot is evenly above 1200 °C, and finally forging, the processing cycle is very long; 2) Method 2: For some heavy steel ingots, the steel ingot is first poured, and the steel ingot is placed The ingot mold is cooled until the riser is completely solidified, and then the mold is released.
  • the temperature of the ingot is generally 700-900 ° C.
  • the warm steel ingot is placed in a heat preservation tank and sent to a heating furnace for heating, so that the temperature inside and outside the steel ingot is uniformly above 1200 ° C, and finally forging is performed. To some extent, it saves heating energy and shortens the processing flow; 3)
  • AlN precipitates along the as-cast coarse austenite grain boundary at 850-950 °C, weakening the grain boundary, and immediately red Sending heat, austenite decomposition and austenitization two phase transitions occur in a short time, which is easy to cause surface cracks.
  • the steel ingot has to be cooled to 200-300 ° C, and then heated, and the residual temperature of the steel ingot is lost. Causes great waste.
  • a soft reduction technique has been developed in the field of continuous casting blanks, which compensates for the solidification shrinkage of the slab by applying a certain amount of reduction in the vicinity of the end of the continuous casting/slab wick. .
  • it can eliminate or reduce the internal void formed by the shrinkage of the slab, prevent the molten steel with intergranular enrichment of solute elements from flowing to the center of the slab; on the other hand, the extrusion caused by the light pressing can also promote the center of the sap
  • the enriched solute element molten steel flows in the opposite direction of the casting direction, so that the solute elements are redistributed in the molten steel, so that the solidification structure of the casting blank is more uniform and dense, and the center segregation and the center looseness are improved.
  • the soft pressing technique is very important for the selection of the pressing position. If the pressing is too early, the center metal has not yet solidified, and the loose defect will form after the pressing; if the pressing is too late, the metal is in the two-phase region with a higher solid fraction. The fluidity is poor, and dense cracks are likely to occur under small deformation. It is generally believed that when the center solid fraction reaches 0.3 to 0.7, the press will play a good role. At the same time, the choice of reduction is also important. According to the equipment capacity, the general reduction rate is 1 to 3%.
  • the soft reduction technology of continuous casting billet can improve the central quality of ordinary carbon steel and low alloy steel billet to a certain extent, but it can't do anything for alloy steel which must be produced by die casting. In fact, the solidification interval of alloy steel tends to be wider, and the defects such as looseness of center shrinkage and dendrite segregation are more serious. It is necessary to combine the solidification and deformation means to eliminate or reduce the central defects of the billet.
  • the object of the present invention is to provide a steel ingot ultra-high temperature soft core forging method, which can eliminate the metallurgical defects such as shrinkage porosity of the steel ingot, reduce dendrite segregation, and refine the structure. Improve the metallurgical quality and mechanical properties of forgings, shorten the processing cycle, save energy, save materials, improve the service life of the mold, and reduce the purpose of forging.
  • the invention discloses a steel ingot ultra-high temperature soft core forging method, which firstly demolishes the poured steel ingot with a liquid core at a high temperature; then, it is placed in a heat preservation vehicle and is transported to a forging press, and the steel ingot is subjected to high temperature pressure forging, so that the steel ingot is subjected to high temperature pressure forging.
  • the solidified terminal dendrites are fully broken, forming a large number of equiaxed crystal structures, eliminating shrinkage porosity and loosening dendrite segregation; finally, conventional forging is performed to fully refine grains and structures.
  • the steel ingot ultra-high temperature soft core forging method the specific steps are as follows:
  • the first step is to remove the mold at a high temperature; the surface temperature of the ingot after demolding is not lower than 1100 ° C, and the center is 1300 ⁇ 1450 °C;
  • the second step is to close the top of the riser; use a spray or air blower to continuously act on the riser of the steel ingot to completely solidify the top of the riser;
  • the third step is to transfer and equalize the temperature; place the steel ingot in the heat preservation car, transport it to the forging press, and the average temperature is 0.5 to 2 hours, ready for forging;
  • the fourth step is to widen the large anvil; place the ingot on the table of the forging press, and use a wide flat anvil to deform 10 to 50% in the thickness direction;
  • the fifth step is to maintain the pressure at high temperature; after the steel ingot is deformed to the specified size, the wide flat anvil is used to maintain the pressure and continue to act on the steel ingot, the action time is not less than 5 minutes, and the deformation amount is not more than 5%;
  • the steel ingot is forged to the final forging size.
  • the temperature is lower than the final forging temperature, the temperature is returned to the high temperature furnace, and the next forging fire is performed.
  • the steel ingot ultra-high temperature soft core forging method in the first step, the steel ingot demoulding time is determined by computer simulation, the steel ingot mold is designed in two ways, one is reverse taper, that is, “upper down and large” mode, demoulding When the riser box and the body are removed at the same time; the other is a positive taper, that is, the "upper and lower” mode.
  • the boom After pouring, the boom is inserted at the edge of the riser, and after the edge of the riser is solidified, the riser box is removed and passed.
  • the lifting rod removes the steel ingot and the ingot mold.
  • the steel ingot ultra-high temperature soft core forging method in the second step, when the top of the riser is completely solidified, the surface temperature of the riser is lower than 1200 °C.
  • the steel ingot ultra-high temperature soft core forging method in the third step, before the opening and forging, the lowest surface temperature of the steel ingot is not lower than 1000 °C.
  • the steel ingot ultra-high temperature soft core forging method in the fourth step, during the main deformation process, the anvil width deformed by the wide flat anvil should cover the total length of the steel ingot, and once deformed into position, the shrinkage hole looseness defect is closed.
  • the steel ingot ultra-high temperature soft core forging method in the fifth step, after the main deformation is finished, the wide flat anvil is used for holding and micro-deformation, so that the closed defects are sufficiently welded.
  • the steel ingot ultra-high temperature soft core forging method in the sixth step, after the center compaction, the steel ingot is forged to the final forging size, and if the forging fire cannot be formed, the forging fire is formed.
  • the volume will change greatly.
  • the density in liquid state is about 7300 kg/m 3
  • the density in solid state is about 7800 kg/m 3 .
  • Such a large density difference will cause different degrees of shrinkage and loose defects in the as-cast microstructure after solidification.
  • the wider the solid-liquid two-phase zone the more severe the tendency to loosen.
  • the conventional method is to place a riser on the top of the ingot, and through good riser insulation conditions, the metal which maintains the liquid in the riser can replenish the volume shrinkage of the ingot under the action of gravity, thereby reducing the shrinkage cavity, Loose defects.
  • the larger the riser the better the insulation effect, and the better the shrinkage effect on the ingot.
  • shrinkage defects can be alleviated by subsequent forging, but for particularly severe shrinkage defects, especially when the purity of the molten steel is poor, the defect surface is enriched with low melting point materials, and these void defects are more difficult to heal by conventional forging.
  • a very large forging ratio is required to break and disperse the inclusions at the healing interface, resulting in extremely high production costs and unstable product quality.
  • the invention is based on the law of solidification and microstructure evolution of metal under pressure and deformation, and proposes to first demould the steel ingot with a liquid core at a high temperature, the surface temperature is not lower than 1100 ° C, the center is 1300 ⁇ 1450 ° C; Hold the forging and keep the pressure on the ingot.
  • the invention breaks through the method of completely forging and then forging the cast steel ingot, and fully combines the two original separation processes of the ingot and the forging, and creates the steel core with excellent fluidity through the ultra-high temperature liquid core release.
  • the semi-solid structure and the huge temperature difference between the surface and the core, combined with the subsequent heavy pressure and pressure holding process, can achieve forced feeding and pressure solidification, which not only solves the problem of shrinkage, looseness, segregation, and coarse structure in the center of the steel ingot.
  • the metallurgical quality is improved, the weight of the riser is reduced, the heating heat of the forging is reduced, the service life of the mold is prolonged, the processing flow is shortened, and the heat processing cost of the forging is greatly reduced.
  • the internal quality of the material has been greatly improved. Due to the ultra-high temperature deformation of the center of the ingot, the shrinkage porosity is completely eliminated, the dendrite segregation defects are alleviated, and the uniformity of the structure is improved. The central mechanical properties of the large-section forging blank can be close to or even reach the performance level of the surface.
  • the surface quality of steel ingots has been greatly improved. Since there is no need to worry about the problem of looseness of the center shrinkage hole, the pouring temperature and the pouring speed can be increased, and the surface quality of the alloy steel ingot can be greatly improved.
  • High-temperature demoulding can shorten the cooling time by 30 to 50%, and use the waste heat forging to reduce the heating time by 30 to 40%, which greatly improves the production efficiency.
  • the life of the ingot mold can be increased by 1 to 2 times due to the shortened demolding time.
  • the weight of the riser can be reduced by 30-50%, and the ingot is designed to have a shape with a height to diameter ratio of 5 or more. Compared with the traditional high-diameter ratio of 1 ⁇ 2, the utilization rate of the ingot-type lifting material is more than 15%. .
  • FIG. 1 is a schematic view of a forging process of a steel ingot ultra-high temperature soft core according to the present invention; wherein (a) is a steel ingot poured into a ladle, (b) is spray cooled after removing the riser box, and (c) is sent to the ingot in a heat preservation vehicle. And the average temperature, (d) is deformation along the diameter/thickness direction of the ingot, (e) is the pressure after deformation, and (f) is forged to the finished product.
  • Figure 2 is a schematic diagram of the healing process of shrinkage porosity defects during ultra-high temperature deformation; (a) is a loose defect that has just sprouted, (b) is loose under large deformation, and (c) is closed. Under the action of pressure retention, it is decomposed into microscopic pores, and (d) the microscopic pores gradually diffuse and disappear under high temperature and high pressure.
  • Fig. 3 is a schematic view showing the process of breaking and homogenizing dendrites when deformed at an ultrahigh temperature; wherein (a) is a solidified terminal dendrite and a residual liquid, and (b) is a dendrite broken and remelted under a large deformation. Decomposed into a multi-stage discrete structure, which becomes the nucleus of the subsequent solidification of the melt, (c) is an equiaxed crystal structure formed by the near-solidification of the center of the ingot under pressure, and (d) is an equiaxed crystal structure. The temperature below the solidus line is greatly deformed, and a finer equiaxed crystal structure formed after recrystallization occurs.
  • FIG. 4 is a photograph of the metallographic structure of the H13 forging obtained by the ultra-high temperature soft core forging method in the embodiment of the present invention.
  • Figure 5 is a photograph of the metallographic structure of the H13 forging obtained by a conventional forging process in a comparative example of the present invention.
  • the forging process of the ultra-high temperature soft core of the steel ingot of the present invention is as follows: (a) ladle pouring steel ingot ⁇ (b) spray cooling after removing the riser box ⁇ (c) placing the steel ingot into the heat preservation car and sending both Temperature ⁇ (d) deformation along the diameter/thickness direction of the ingot ⁇ (e) holding pressure after deformation ⁇ (f) forging to the finished product.
  • the method of the invention is applicable to carbon manganese steel, low alloy steel, medium and high alloy steel, especially for ultra high temperature soft core forging of steel ingot with wide solidification interval and particularly developed as-cast structure.
  • the steel ingot ultra-high temperature soft core forging method of the present invention firstly demolds the poured ingot with a liquid core at a high temperature; then, it is placed in a heat preservation vehicle and is transported to a forging press, and the steel ingot is carried out with a liquid core.
  • High-temperature pressure forging the solidification end dendrites are fully broken, forming a large number of equiaxed crystal structures, eliminating shrinkage porosity and loosening dendritic segregation; finally, conventional forging such as upsetting and lengthening, and fully refining grains and microstructure; Specific steps are as follows:
  • the first step is to demould the steel ingot with a liquid core at a high temperature, the surface temperature of the ingot is not lower than 1100 ° C (preferably 1150 ° C ⁇ 1250 ° C), and the center temperature is maintained at 1300 ⁇ 1450 ° C;
  • the healing process of the shrinkage porosity defect is as follows: (a) the loose defect just emerging ⁇ (b) the looseness is closed under the large deformation ⁇ (c) the closed looseness is in the continuous holding pressure Under the action of the decomposition into microscopic holes ⁇ (d) microscopic pores gradually diffuse and disappear under high temperature and high pressure. It can be seen from Fig. 2 that the large deformation at the solidification end of the steel ingot can accelerate the high-temperature diffusion of the closed interface of the hole, and the defect of the loose-hole defect is efficiently healed, thereby increasing the density of the material.
  • the large deformation at the solidification end of the ingot can more fully break the dendrites, form a larger number of smaller equiaxed grains, and further refine the material structure. Reduce dendrite segregation and promote uniform composition.
  • the second step is to use a spray or air blower to continuously act on the riser of the steel ingot to completely solidify the top of the riser;
  • the steel ingot is placed in the heat preservation car and transported to the forging press at an average temperature of 0.5 to 2 hours;
  • the steel ingot is placed on the table of the forging press, and the wide flat anvil is deformed by 10 to 50% along the diameter (thickness) direction;
  • the wide flat anvil is used to maintain the pressure and continue to act on the steel ingot, the action time is not less than 5 minutes, and the deformation amount is not more than 5%;
  • the steel ingot is forged to the final forging size.
  • the temperature is lower than the final forging temperature, the temperature is returned to the high temperature furnace, and the next forging fire is performed.
  • the demolding time of the ingot is determined by computer simulation.
  • the ingot mold is designed in two ways, one is the reverse taper, that is, the “upper and lower” mode, and the riser box and the ingot are simultaneously removed during demolding;
  • the other type is a positive taper, that is, a "upper and lower” mode.
  • a spray or air blower is used to continuously act on the riser of the steel ingot to completely solidify the top of the riser, and the surface temperature is lower than 1200 ° C (preferably 1100 ° C ⁇ 1180 ° C).
  • the steel ingot is placed in the heat preservation car for 0.5 to 2 hours, and is transported to the forging press.
  • the lowest surface temperature of the ingot before the forging is not less than 1000 ° C (preferably 1100 ° C to 1250 ° C).
  • a wide flat anvil should be used.
  • the width of the anvil should cover the total length of the ingot, and the deformation rate is 10 to 50% (preferably 20 to 50%). Once the deformation is in place, the shrinkage porosity is closed. ;
  • the wide flat anvil is used for holding pressure and slow micro-deformation, the pressure action time is not less than 5 minutes (preferably 5 to 10 minutes), and the deformation amount is not more than 5% (preferably 1 to 5). %), so that the closed defects are sufficiently welded.
  • the steel ingot is forged to the final forging size. If the fire cannot be formed, the fire forming may be increased.
  • the smelting and pouring ingot has a weight of 9 tons, a rectangular cross section, and a size of 720 ⁇ 1080 ⁇ 1450mm.
  • the material is H13 steel.
  • the measured components are shown in Table 1.
  • the first step is to remove the mold at an extremely high temperature. After the ingot is poured for 3.5 hours, the riser protection slag is blown off, so that the steel ingot is released from the liquid core at a high temperature, the surface temperature of the ingot is 1230 ° C, and the center temperature of the ingot is maintained above 1350 ° C.
  • the second step is to close the top of the riser.
  • the sprinkler is used to continuously act on the riser of the steel ingot for 10 min, so that the top of the riser is completely solidified, and the surface temperature is 1180 °C.
  • the third step is transshipment and temperature equalization.
  • the steel ingot is placed in the heat preservation car, and transported to the forging press in 30 minutes. After the average temperature is 30 minutes, the minimum temperature of the steel ingot surface is 1100 ° C, and the maximum temperature of the steel ingot surface is 1250 ° C. At this time, the steel car is separated from the heat preservation car and ready for forging.
  • the fourth step is the wide anvil deformation.
  • the steel ingot was placed on the table of the forging press, and the wide flat anvil was deformed by 240 mm in the thickness direction to be deformed once.
  • the fifth step is to keep the pressure at high temperature. After the steel ingot is deformed to the specified size, the wide flat anvil is used to maintain the pressure and continue to act on the steel ingot. The action time is 10 min, and the deformation amount is 3%, so that the closed defects are sufficiently welded.
  • the section of the ingot is drawn to 800 ⁇ 800 mm, and the chamfered to the height is 1200 mm, and the length is ⁇ 450 mm.
  • Comparative Example 1 uses a conventional steel ingot after complete solidification, demolding, annealing and reheating and forging processes, the specific steps are as follows:
  • the first step is to release the mold at medium temperature. After the ingot was poured for 8 hours, the ingot and the riser were completely solidified, and the ingot was demolded, and the surface temperature of the ingot was 700 °C.
  • the second step is high temperature annealing.
  • the steel ingot was placed in a heating furnace at 850 ° C, and after 15 hours of heat preservation, it was slowly cooled to a surface temperature of 300 ° C.
  • the third step is transshipment.
  • the ingot was placed in a heat preservation car, transported to a forging press in 30 minutes, then slowly heated to 850 ° C, and after 5 hours of heat preservation, slowly heated to 1230 ° C, ready for forging.
  • the fourth step is the first fire forging.
  • the ingot is upset 50% in the height direction, and then elongated to a section size of 800 ⁇ 800 mm, chamfered and then heated into the furnace.
  • the fifth step the second fire forging.
  • the ingot is upset 50% in the height direction, and then elongated to a section size of 800 ⁇ 800 mm, chamfered and then heated into the furnace.
  • the sixth step the third fire forging. Pull the steel ingot to ⁇ 450mm.
  • Example 1 and Comparative Example 1 were subjected to isothermal spheroidization treatment, respectively, incubated at 850 ° C and 750 ° C for 5 h, and slowly cooled to room temperature.
  • the center sample of the forging was taken, and the microstructure of the sample was measured by a metallographic microscope. Analysis, the specific metallographic organization is shown in Figure 4 and Figure 5. As can be seen from the figure, the structure in the examples was sufficiently refined, and the average grain size was only 10 ⁇ m, while the large crystal grains of 100 ⁇ m were still present in the comparative example.
  • the carbide distribution in the examples was very uniform, and there was no liquid carbonization, and the carbides in the comparative examples were segregated, unevenly distributed, and a small amount of liquid carbides.
  • the microstructure state of the post-forging heat treatment fully demonstrates that the conventional forging process is difficult to completely eliminate the liquid precipitation carbide, and the structure is coarse and the secondary carbide distribution is not uniform, and the ultra-high temperature soft core forging method of the present invention can effectively eliminate the liquid precipitation carbide.
  • the uniform fine crystal grains and the finely dispersed secondary carbides are obtained, so that the service life of the mold steel can be greatly improved.

Landscapes

  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Forging (AREA)

Abstract

La présente invention concerne un procédé de forgeage pour noyau mou à ultra-haute température d'un lingot d'acier, comprenant les étapes suivantes : dans un premier temps, soumission d'un lingot d'acier coulé pourvu d'un noyau liquide à un démoulage à ultra-haute température ; ensuite, mise en place dudit lingot dans une cabine de maintien de température à une température uniforme, et transport du lingot dans une presse à forger ; soumission du lingot d'acier pourvu du noyau liquide à un forgeage à haute température et maintien de pression, pour écraser complètement les dendrites au niveau de l'extrémité de solidification, afin de former une grande quantité de structures à cristaux équiaxiaux, d'éliminer la porosité de retrait et le relâchement, et d'atténuer la ségrégation de cristaux dendritiques ; enfin, réalisation d'un forgeage classique pour affiner entièrement les structures et grains cristallins. Le procédé mentionné ci-dessus constitue une percée par rapport aux procédés classiques de forgeage de lingots d'acier coulés uniquement après solidification complète. Le démoulage à ultra-haute température d'un lingot d'acier pourvu d'un noyau liquide crée une structure à l'état semi-solide présentant une excellente fluidité dans le noyau du lingot d'acier et une grande différence de température entre la surface et le noyau. Suite à l'association ultérieure entre une forte pressurisation et un procédé de maintien de pression, on peut obtenir une alimentation forcée et une solidification sous pression, ce qui permet non seulement de résoudre les problèmes de porosités de retrait, de relâchement, de ségrégation etc. au centre du lingot d'acier pour améliorer la qualité métallurgique, mais également de réduire le poids de la colonne montante et le nombre de cycles de chauffage pour le forgeage, et de prolonger la durée de vie du moule.
PCT/CN2014/092623 2014-07-21 2014-11-29 Procédé de forgeage pour noyau mou à ultra-haute température d'un lingot d'acier Ceased WO2016011759A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN201410349152.2 2014-07-21
CN201410349152.2A CN105268884B (zh) 2014-07-21 2014-07-21 一种钢锭超高温软芯锻造方法

Publications (1)

Publication Number Publication Date
WO2016011759A1 true WO2016011759A1 (fr) 2016-01-28

Family

ID=55139219

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2014/092623 Ceased WO2016011759A1 (fr) 2014-07-21 2014-11-29 Procédé de forgeage pour noyau mou à ultra-haute température d'un lingot d'acier

Country Status (2)

Country Link
CN (1) CN105268884B (fr)
WO (1) WO2016011759A1 (fr)

Cited By (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107695163A (zh) * 2017-10-10 2018-02-16 上海新闵（东台）重型锻造有限公司 核岛蒸发器封头整体冲压成型装置及冲压成型方法
CN110131563A (zh) * 2018-02-08 2019-08-16 中国科学院金属研究所 一种适用于超高温软芯锻造用钢锭锭型设计方法
CN110263418A (zh) * 2019-06-17 2019-09-20 哈尔滨理工大学 一种体心立方合金微观偏析数值预测方法
CN112275978A (zh) * 2020-09-09 2021-01-29 广州锻造一厂股份有限公司 一种防裂金属钢柱的锻造方法
CN114012008A (zh) * 2021-10-10 2022-02-08 河南中原特钢装备制造有限公司 大规格022Cr23Ni5Mo3N锻件的生产工艺
CN114438298A (zh) * 2022-02-21 2022-05-06 中国科学院金属研究所 一种高温扩散方法及一种合金钢
CN114558968A (zh) * 2022-01-28 2022-05-31 欧拉姆阀门科技有限公司 一种连续多级进料连锻成型工艺
CN114888216A (zh) * 2022-04-28 2022-08-12 重庆大学 一种微观组织及力学性能梯度分布的钢铁壳体构件及成形方法
CN115354130A (zh) * 2022-09-15 2022-11-18 湖北上大模具材料科技股份有限公司 一种热作模具钢复合细化晶粒的方法
CN115889647A (zh) * 2022-10-14 2023-04-04 石钢京诚装备技术有限公司 一种改善热作模具钢h13碳偏析的锻造方法
CN117181970A (zh) * 2023-08-04 2023-12-08 太原重工股份有限公司 25Cr2Ni4MoV钢转子锻件加工方法
CN117512280A (zh) * 2023-11-28 2024-02-06 无锡继平新材料科技有限公司 一种船用高速桨轴的锻造及热处理工艺
CN118122928A (zh) * 2024-03-05 2024-06-04 太原重工股份有限公司 大型火电汽轮机用Cr-Ni-Mo-V钢实心整体转子体锻件的加工方法

Families Citing this family (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109513887B (zh) * 2017-09-20 2020-10-16 中国科学院金属研究所 一种适用于超高温软芯锻造用常规锭型钢锭的处理方法
CN108097854B (zh) * 2017-12-04 2019-12-13 北京科技大学 一种大型金属构件高均匀性短流程成形方法
CN110129548B (zh) * 2018-02-08 2020-11-13 中国科学院金属研究所 一种适用于钢锭超高温热送及加热工艺设计方法
CN110315018B (zh) * 2018-03-29 2020-08-21 中国科学院金属研究所 高效率消除坯料内部孔洞型缺陷的超高温软芯锻造方法
CN109719241B (zh) * 2018-11-21 2020-08-14 兰州兰石能源装备工程研究院有限公司 一种钢的短流程铸锻一体化工艺
CN109834112A (zh) * 2019-02-26 2019-06-04 江苏飞达环保科技有限公司 一种中厚板铸轧生产线
CN110512061B (zh) * 2019-09-27 2020-12-01 江阴华润制钢有限公司 一种连铸坯直锻生产模具钢的工艺方法
CN111041371B (zh) * 2019-12-31 2021-09-14 北京科技大学 一种轻质高强钢及半固态液芯锻造方法
CN112517862B (zh) * 2020-11-20 2022-01-14 中国科学院金属研究所 一种大尺寸高温合金母合金铸锭的二次缩孔控制方法
CN113953421B (zh) * 2021-10-21 2024-02-23 浙江大隆特材有限公司 一种核电管道用316ln锻圆钢及其制备方法
CN114277226B (zh) * 2021-12-10 2024-05-03 江苏铸鸿锻造有限公司 一种纵裂敏感钢锭免退火温装连续炉的锻制圆钢方法

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0119365A1 (fr) * 1983-03-14 1984-09-26 Thomas Di Serio Procédé pour fabriquer des pièces en aluminium ou en alliage d'aluminium
CN102886501A (zh) * 2012-10-09 2013-01-23 中国科学院金属研究所 一种宽厚板轧机用宽厚板坯高效制备工装和制备方法
CN103008577A (zh) * 2012-12-07 2013-04-03 中国科学院金属研究所 微缺陷高利用率优质模铸钢锭的制备方法和模具
CN103305764A (zh) * 2013-06-26 2013-09-18 攀钢集团江油长城特殊钢有限公司 冷作模具圆钢及其制造方法
JP2013221181A (ja) * 2012-04-17 2013-10-28 Hiroshima Univ 金属間化合物強化複合材料及びその製造方法
CN203639530U (zh) * 2013-01-11 2014-06-11 上海大学 利用稳恒磁场优化金属凝固组织的复合电渣熔铸装置

Family Cites Families (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5118930A (ja) * 1974-08-08 1976-02-14 Mitsui Mining & Smelting Co Ingotsutotsumikasanesochi
CN102166637B (zh) * 2010-11-26 2013-01-02 中国科学院金属研究所 一种消除连铸钢锭中心缩孔和疏松的方法
CN103691860B (zh) * 2013-12-06 2015-10-07 天津重型装备工程研究有限公司 有效提高大锻件质量的加工方法

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0119365A1 (fr) * 1983-03-14 1984-09-26 Thomas Di Serio Procédé pour fabriquer des pièces en aluminium ou en alliage d'aluminium
JP2013221181A (ja) * 2012-04-17 2013-10-28 Hiroshima Univ 金属間化合物強化複合材料及びその製造方法
CN102886501A (zh) * 2012-10-09 2013-01-23 中国科学院金属研究所 一种宽厚板轧机用宽厚板坯高效制备工装和制备方法
CN103008577A (zh) * 2012-12-07 2013-04-03 中国科学院金属研究所 微缺陷高利用率优质模铸钢锭的制备方法和模具
CN203639530U (zh) * 2013-01-11 2014-06-11 上海大学 利用稳恒磁场优化金属凝固组织的复合电渣熔铸装置
CN103305764A (zh) * 2013-06-26 2013-09-18 攀钢集团江油长城特殊钢有限公司 冷作模具圆钢及其制造方法

Cited By (19)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107695163A (zh) * 2017-10-10 2018-02-16 上海新闵（东台）重型锻造有限公司 核岛蒸发器封头整体冲压成型装置及冲压成型方法
CN107695163B (zh) * 2017-10-10 2023-06-16 上海新闵（东台）重型锻造有限公司 核岛蒸发器封头整体冲压成型装置及冲压成型方法
CN110131563A (zh) * 2018-02-08 2019-08-16 中国科学院金属研究所 一种适用于超高温软芯锻造用钢锭锭型设计方法
CN110263418B (zh) * 2019-06-17 2022-10-21 哈尔滨理工大学 一种体心立方合金微观偏析数值预测方法
CN110263418A (zh) * 2019-06-17 2019-09-20 哈尔滨理工大学 一种体心立方合金微观偏析数值预测方法
CN112275978A (zh) * 2020-09-09 2021-01-29 广州锻造一厂股份有限公司 一种防裂金属钢柱的锻造方法
CN114012008A (zh) * 2021-10-10 2022-02-08 河南中原特钢装备制造有限公司 大规格022Cr23Ni5Mo3N锻件的生产工艺
CN114012008B (zh) * 2021-10-10 2023-08-25 河南中原特钢装备制造有限公司 大规格022Cr23Ni5Mo3N锻件的生产工艺
CN114558968A (zh) * 2022-01-28 2022-05-31 欧拉姆阀门科技有限公司 一种连续多级进料连锻成型工艺
CN114558968B (zh) * 2022-01-28 2024-05-14 欧拉姆阀门科技有限公司 一种连续多级进料连锻成型工艺
CN114438298A (zh) * 2022-02-21 2022-05-06 中国科学院金属研究所 一种高温扩散方法及一种合金钢
CN114438298B (zh) * 2022-02-21 2022-11-15 中国科学院金属研究所 一种高温扩散方法及一种合金钢
CN114888216A (zh) * 2022-04-28 2022-08-12 重庆大学 一种微观组织及力学性能梯度分布的钢铁壳体构件及成形方法
CN115354130B (zh) * 2022-09-15 2024-03-12 湖北上大模具材料科技股份有限公司 一种热作模具钢复合细化晶粒的方法
CN115354130A (zh) * 2022-09-15 2022-11-18 湖北上大模具材料科技股份有限公司 一种热作模具钢复合细化晶粒的方法
CN115889647A (zh) * 2022-10-14 2023-04-04 石钢京诚装备技术有限公司 一种改善热作模具钢h13碳偏析的锻造方法
CN117181970A (zh) * 2023-08-04 2023-12-08 太原重工股份有限公司 25Cr2Ni4MoV钢转子锻件加工方法
CN117512280A (zh) * 2023-11-28 2024-02-06 无锡继平新材料科技有限公司 一种船用高速桨轴的锻造及热处理工艺
CN118122928A (zh) * 2024-03-05 2024-06-04 太原重工股份有限公司 大型火电汽轮机用Cr-Ni-Mo-V钢实心整体转子体锻件的加工方法

Also Published As

Publication number Publication date
CN105268884B (zh) 2017-04-19
CN105268884A (zh) 2016-01-27

Similar Documents

Publication Publication Date Title
WO2016011759A1 (fr) Procédé de forgeage pour noyau mou à ultra-haute température d'un lingot d'acier
CN105436368B (zh) 提高工模具钢组织均匀性的超高温交叉大变形锻造方法
Deng et al. Recent research on the deformation behavior of particle reinforced magnesium matrix composite: a review
CN101624671B (zh) 一种大直径7005铝合金圆铸锭及其制备方法
CN113136497B (zh) 一种高强耐应力腐蚀的铝合金型材的制备方法
CN106077558A (zh) 一种铝合金半固态挤压铸造的方法及系统
CN101914713A (zh) 超大规格高强耐热镁合金锭坯半连续铸造工艺
CN101787472A (zh) 耐热锻压镁稀土合金及其制备方法
CN101255517A (zh) 一种镁合金
CN115055654B (zh) 高碳钢盘条及其生产方法
CN102699081A (zh) 一种铝硅铁合金发动机缸套的半固态触变挤压成形方法
CN111957924A (zh) 一种变形镁合金铸锭坯的铸造装置和低压反重力铸造方法
CN105695779A (zh) 一种高精度和高洁净度合金铝棒的制备方法
CN110042238A (zh) 高品质FeV50合金的生产方法
CN108097854B (zh) 一种大型金属构件高均匀性短流程成形方法
CN101147968B (zh) 低温剪切流变压铸工艺
CN102409187B (zh) 电流制备半固态金属浆/坯料的方法及装置
CN115896509B (zh) 一种在镁合金中构筑超细晶组织的制备方法
CN103934437B (zh) 初生硅细化的高硅铝合金流变浆料的制备方法
Zhang et al. Forming properties and microstructure of Al-Cu alloy prepared by liquid-die forging
CN108015255B (zh) 一种高速工具钢的制备方法
CN101871068A (zh) 一种含锡与铝的高强度高塑性镁合金及其制备方法
CN107199321B (zh) 一种时变控制半固态成形工艺
CN102161090A (zh) 一种提高厚大断面铸坯自补缩能力的方法
Reis et al. Thixoforging of Al–3.8% Si alloy recycled from aluminum cans

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 14897994

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 14897994

Country of ref document: EP

Kind code of ref document: A1