CN110684913B - Preparation method of ultrahigh-strength and high-toughness aluminum alloy - Google Patents

Preparation method of ultrahigh-strength and high-toughness aluminum alloy Download PDF

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CN110684913B
CN110684913B CN201910965752.4A CN201910965752A CN110684913B CN 110684913 B CN110684913 B CN 110684913B CN 201910965752 A CN201910965752 A CN 201910965752A CN 110684913 B CN110684913 B CN 110684913B
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aluminum alloy
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melt
temperature
alloy
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CN110684913A (en
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章国伟
陈伟
韩震
杜喜望
辛海鹰
翟景
马波
马力
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China Weapon Science Academy Ningbo Branch
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/10—Alloys based on aluminium with zinc as the next major constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/115—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by spraying molten metal, i.e. spray sintering, spray casting
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/20—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by extruding
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/026—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/03—Making non-ferrous alloys by melting using master alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/0408—Light metal alloys
    • C22C1/0416—Aluminium-based alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/053—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with zinc as the next major constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/20—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces by extruding
    • B22F2003/208—Warm or hot extruding

Abstract

A preparation method of an ultrahigh-strength and high-toughness aluminum alloy comprises the following steps: weighing raw materials according to the component and content design; putting pure Al, Al-50Cu intermediate alloy and Al-Ni intermediate alloy into a medium-frequency induction furnace, heating until metal in a crucible is molten, adding Zr particles and pure Mn sheets when the temperature is raised to 720-740 ℃, raising the temperature to 800-820 ℃, and pressing pure Zn and pure Mg into the crucible by using a graphite press spoon after power failure; adopting refining agent and alterant and C2Cl6The degasifier is used for modification and refining; slagging off and standing; pouring the melt into a spray deposition device, opening a powder feeding device, feeding low-alloy aluminum alloy powder with the content of 5% -30% into a spray deposition atomizing cone, and performing spray deposition to form a billet; performing extrusion densification treatment and effective heat treatment. The method has the advantages of simple process, short preparation process time, reliable process, great saving of production cost, improvement of production efficiency and easiness in large-scale industrial production, and the prepared aluminum alloy has higher strength and toughness.

Description

Preparation method of ultrahigh-strength and high-toughness aluminum alloy
Technical Field
The invention belongs to the technical field of aluminum alloy materials, and relates to a preparation method of an ultrahigh-strength and high-toughness aluminum alloy.
Background
The 7000 series aluminum alloy is a high-strength and high-toughness aluminum alloy material which is developed and developed internationally in the 40 th century with aeronautical materials as backgrounds, and the traditionally used 7000 series aluminum alloy material is generally a final various section products obtained through procedures of ingot casting, cold-hot deformation processing, heat treatment and the like, is widely used for manufacturing various airplane fuselages, wing spars, cabin wall panels, rocket medium-high-strength structural parts and the like for a long time, and is an indispensable important material in the aerospace industry of various countries in the world. At present, dozens of 7000 series aluminum alloy products with different alloy composition standard brands are developed all over the world, and the corresponding alloy heat treatment standard process reaches hundreds of products. In long-term scientific research, researchers find that the comprehensive performance of the alloy can be effectively improved by increasing the content of Zn element in 7000 series aluminum alloy, but when the content of Zn element in the alloy exceeds 8%, because the crystallization range of the alloy is wide and the specific gravity difference between a precipitated phase and a matrix is large, when the aluminum alloy with high Zn content is produced by adopting the traditional process, the crystal grains in the alloy are easy to be coarse, obvious macro-segregation exists, and the heat cracking phenomenon is easy to generate in an ingot, so the Zn content of 7000 series aluminum alloy produced by adopting the traditional process is generally not more than 8%, and meanwhile, the ultimate tensile strength of 7000 series aluminum alloy produced by adopting the traditional process is difficult to break through the relationship of 700 MPa.
The occurrence of the spray deposition technology enables the industry of various countries to break through the limitation of the traditional 8% Zn content, and the research and development of new generation 7000 series ultrahigh strength aluminum alloy becomes practical, when the spray deposition technology is adopted to prepare the aluminum alloy with the Zn content exceeding 8%, because crystal grains in the alloy are obviously refined, various macro and micro segregation are inhibited, the tendency of generating heat cracks inside the deposited blank in the solidification process can be effectively controlled, meanwhile, because the solidification speed is accelerated, the supersaturation degree of various alloy elements in the blank is increased, the precipitation of various precipitated phases in the subsequent heat treatment process is more sufficient, and the material is beneficial to obtaining more excellent mechanical properties.
Densification of spray-formed ultrahigh-strength aluminum alloy materialThe final forming generally adopts large deformation modes such as extrusion, rolling, forging and the like, and because the material is subjected to large shearing deformation, an oxide film on the surface of powder in a deposition layer is thoroughly crushed, and the material can be completely compact and reach the degree of metallurgical bonding. In the large deformation process, the internal structure of the material can also generate cooperative deformation, such as grain elongation, reinforcing phase streamline arrangement and the like, and the process can cause the formed part to have anisotropy, thereby influencing subsequent application. Moreover, improper deformation can also form crack defects inside, affecting its performance. Meanwhile, the pursuit of high strength inevitably leads to lower plasticity and toughness of the alloy, for example, the tensile strength of typical spray-deposited ultrahigh-strength aluminum alloy can reach more than 800MPa, but the fracture toughness is only 15 MPa.m1/2And the application of the material is seriously influenced.
Therefore, a preparation method of the ultrahigh-strength and high-toughness aluminum alloy needs to be developed to meet the requirement of aviation materials, and the technology for preparing the ultrahigh-strength and high-toughness aluminum alloy by adopting a spray deposition technology is not reported at present.
Disclosure of Invention
The invention aims to solve the technical problem of providing a preparation method of an ultrahigh-strength and high-toughness aluminum alloy, which has simple process and high production efficiency, and adopts a spray deposition technology to prepare the aluminum alloy, so that the strength and the toughness of the prepared aluminum alloy are kept at higher levels.
The technical scheme adopted by the invention for solving the technical problems is as follows: the preparation method of the ultrahigh-strength high-toughness aluminum alloy is characterized by comprising the following steps of:
1) weighing the raw materials according to the chemical components Al- (10-14) Zn- (1.8-3.2) Mg- (0.8-2.0) Cu- (0.15-0.4) Zr- (0.05-0.3) Mn- (0.05-0.3) Ni of the designed ultrahigh-strength and high-toughness aluminum alloy: zn; mg; cu; zr; mn; ni; al; wherein, Cu adopts Al-50Cu intermediate alloy, Ni adopts Al-20Ni intermediate alloy, and the rest is pure metal;
2) putting the weighed pure Al, Al-50Cu intermediate alloy and Al-Ni intermediate alloy into a medium-frequency induction furnace, electrifying and heating until the metal in the crucible is melted, heating the melt to 720-740 ℃, adding Zr particles and pure Mn sheets, fully stirring, heating the melt to 800-820 ℃, pressing pure Zn and pure Mg by a graphite pressure spoon after power failure, fully stirring, and heating the melt to 720-750 ℃;
3) adopting proper amount of refining agent and alterant and C2Cl6The degassing agent is used for modifying and refining the melt; after treatment, slagging off the melt, then standing the melt for 10-15 min, and raising the temperature of the melt to 810-850 ℃;
4) pouring the melt into a spray deposition device, simultaneously opening a powder feeding device, feeding low-alloy aluminum alloy powder with the content of 5-30% into a spray deposition atomizing cone, and performing spray deposition to form a billet;
5) carrying out extrusion densification treatment on the spray deposition billet, wherein the extrusion ratio is 8-10: 1, the extrusion temperature is 420-450 ℃;
6) carrying out peak aging heat treatment on the bar stock, wherein the heat treatment process is solid solution treatment: keeping the temperature of 445-455 ℃ for 0.5-1.5 h and keeping the temperature of 470-480 ℃ for 1-3 h, and then performing water quenching at room temperature; aging treatment: and (3) preserving the heat for 23-25 hours at the temperature of 110-130 ℃, and then carrying out mechanical property test.
Preferably, the ultrahigh-strength and high-toughness aluminum alloy obtained in the step 1) comprises the following chemical components: al- (10-14) Zn- (1.8-3.2) Mg- (0.8-2.0) Cu- (0.15-0.4) Zr- (0.05-0.3) Mn- (0.05-0.3) Ni.
Preferably, the refining agent in the step 3) is HGJ-1, the modifier is HGPB-1, and the weight percentage of the refining agent and the modifier is 0.4-0.6%.
Further, the low-alloying aluminum alloy powder in the step 4) can adopt one or more of 7075 aluminum alloy powder, 7055 aluminum alloy powder or pure Al powder.
Still further, the low-alloyed aluminum alloy powder of the step 4) needs to be pretreated before being added to remove water and gas attached to the powder.
Preferably, the extrusion ratio of the step 5) is 9: 1.
finally, the solution treatment in the step 6): preserving heat at 450 ℃ for 1h +475 ℃ for 2h, and carrying out aging treatment: the temperature is kept at 120 ℃ for 24 hours.
Compared with the prior art, the invention has the advantages that: in the jet sinkIn the process of deposition, 5-30% of low-alloying aluminum alloy powder is added into an atomizing cone through a powder feeding device, so that low-component alloy powder is distributed in an ultrahigh-strength aluminum alloy matrix, a billet is densified and deformed in the subsequent heat treatment process, solute atoms are diffused due to concentration difference, the grain boundary of the alloy is subjected to diffusion offset, and meanwhile, residual stress is relaxed at the position, so that the fracture toughness of the alloy is improved, and the strength of the alloy is not obviously reduced. The preparation process is simple, the tensile strength of the prepared aluminum alloy is maintained above 780MPa, and the fracture toughness of the alloy is maintained at 30 MPa-m1/2Compared with other aluminum alloys with similar performance levels, the preparation method has the advantages of short preparation process time and reliable process, greatly saves the production cost, improves the production efficiency and is easy for large-scale industrial production.
Drawings
FIG. 1 is a metallographic structure of an aluminum alloy prepared by comparative example according to the present invention after heat treatment;
FIG. 2 is a scanned structure view of an aluminum alloy prepared in a comparative example after heat treatment;
FIG. 3 is a metallographic structure diagram of an aluminum alloy prepared by adding 5% low-alloy aluminum alloy powder in example 1 after heat treatment;
FIG. 4 is a graph of the scanned structure of the aluminum alloy prepared by adding 5% low-alloyed aluminum alloy powder in example 1 after heat treatment;
FIG. 5 is a metallographic structure diagram of the aluminum alloy prepared by adding 30% low-alloy aluminum alloy powder in example 2 after heat treatment;
FIG. 6 is a scanned texture map of the aluminum alloy prepared by adding 30% low-alloyed aluminum alloy powder to example 2 after heat treatment.
Detailed Description
The invention is described in further detail below with reference to the accompanying examples.
Comparative example (no addition of low alloyed aluminum alloy powder):
pure Al and pure Zn are weighed according to the designed ultra-high strength aluminum alloy components Al- (10-14) Zn- (1.8-3.2) Mg- (0.8-2.0) Cu- (0.15-0.4) Zr- (0.05-0.3) Mn- (0.05-0.3) Ni,pure Mg, Al-50Cu intermediate alloy, Al-20Ni intermediate alloy, Zr particles, pure Mn sheets and the like accounting for 120KG, putting the weighed alloy comprising the pure Al, the Al-50Cu intermediate alloy and the Al-Ni intermediate alloy into a medium-frequency induction furnace, electrifying and heating until metal in a crucible is melted, adding the Zr particles and the pure Mn sheets when the temperature of a melt is raised to 720-740 ℃, raising the temperature of the melt to 800-820 ℃ after fully stirring, pressing pure Zn and pure Mg into the melt by a graphite pressing spoon after power failure, fully stirring, and raising the temperature of the melt to 720-750 ℃; refining agent, modifier (0.5 wt%) and C are used2Cl6The degasifier is used for modifying and refining the melt. Slagging off the melt after treatment, standing the melt for 10-15 min, and raising the temperature of the melt to 810-850 ℃; pouring the melt into a spray deposition device for spray deposition; and (3) carrying out extrusion densification treatment on the spray deposition billet, wherein the extrusion ratio is 9: 1, the extrusion temperature is 420-450 ℃; carrying out peak aging heat treatment on the bar stock, wherein the specific heat treatment process is solid solution treatment: 1h at 450 ℃ and 2h at 475 ℃, and then performing water quenching at room temperature; aging treatment: the temperature is kept at 120 ℃ for 24 hours. And then carrying out mechanical property test.
FIGS. 1 and 2 are metallographic structures and scanning structure diagrams of the aluminum alloys prepared in the comparative example in a peak aged state.
As can be seen from fig. 1 and 2, after the spray-deposited ultra-high strength aluminum alloy without low-alloying powder is subjected to peak aging treatment, the grain boundaries are elongated in the extrusion direction, and the grain boundaries are flat and do not diffuse or shift. Mechanical property tests show that the tensile strength, the yield strength, the elongation and the fracture toughness of the alloy are respectively 800MPa, 735MPa, 5 percent and 15 MPa.m1/2It can be seen that although the strength of the alloy is high, its elongation and fracture toughness are low, thus limiting further applications of the material.
Example 1 (adding 5% low alloyed aluminum alloy powder)
Weighing pure Al, pure Zn, pure Mg, Al-50Cu intermediate alloy, Al-20Ni intermediate alloy, Zr particles, pure Mn sheets and the like according to the designed ultrahigh-strength aluminum alloy component Al- (10-14) Zn- (1.8-3.2) Mg- (0.8-2.0) Cu- (0.15-0.4) Zr- (0.05-0.3) Mn- (0.05-0.3) Ni, and packaging the weighed alloy into a bag with the total weight of 120KGPutting pure Al, Al-50Cu intermediate alloy and Al-Ni intermediate alloy into a medium-frequency induction furnace, electrifying and heating until metal in a crucible is melted, adding Zr particles and pure Mn sheets when the temperature of a melt is raised to 720-740 ℃, raising the temperature of the melt to 800-820 ℃ after fully stirring, pressing pure Zn and pure Mg into the melt by a graphite pressure spoon after power is off, fully stirring, and raising the temperature of the melt to 720-750 ℃; refining agent, modifier (0.5 wt%) and C are used2Cl6The degasifier is used for modifying and refining the melt. Slagging off the melt after treatment, standing the melt for 10-15 min, and raising the temperature of the melt to 810-850 ℃; pouring the melt into a spray deposition device, simultaneously opening a powder feeding device, feeding low-alloy flower aluminum alloy powder with the content of 5% into a spray deposition atomizing cone, and performing spray deposition to form a billet; and (3) carrying out extrusion densification treatment on the spray deposition billet, wherein the extrusion ratio is 9: 1, the extrusion temperature is 420-450 ℃; carrying out peak aging heat treatment on the bar stock, wherein the specific heat treatment process is solid solution treatment: 1h at 450 ℃ and 2h at 475 ℃, and then performing water quenching at room temperature; aging treatment: preserving the heat for 24 hours at 120 ℃; and then carrying out mechanical property test.
Wherein, the low-alloying aluminum alloy powder can adopt one or more of 7075 aluminum alloy powder, 7055 aluminum alloy powder and pure Al powder; the low-alloyed aluminum alloy powder needs to be pretreated before addition to remove water and gases adhering to the powder.
FIGS. 3 and 4 are metallographic structures and scanned structure diagrams of the aluminum alloy prepared in example 1 in the peak aged state.
As can be seen from fig. 3 and 4, after 5% low-alloying aluminum alloy powder is added into the billet, the grain boundaries are elongated in the extrusion direction as a whole, but part of the grain boundaries are diffused and shifted, namely part of the grain boundaries are diffused into adjacent grains and are in a sawtooth shape, so that the alloy needs to consume more energy when being fractured, and the fracture toughness of the alloy is improved. Mechanical property tests show that the tensile strength, the yield strength, the elongation and the fracture toughness of the alloy are 793MPa, 725MPa, 7.5 percent and 31 MPa-m respectively1/2. Therefore, the plasticity and the toughness of the alloy are greatly improved.
Example 2 (adding 30% low alloyed aluminum alloy powder)
The difference from example 1 is that: the addition of the low-alloying aluminum alloy powder is 30 percent, and the spray deposition billet is subjected to densification extrusion and peak aging treatment.
FIGS. 5 and 6 are metallographic structures and scanned structure diagrams of the alloy prepared in example 1 in the peak aged state.
As can be seen from fig. 5 and 6, after 30% of low-alloying aluminum alloy powder is added into the billet, the grain boundaries are still elongated in the extrusion direction as a whole, but a large part of the grain boundaries are diffused and shifted, namely, part of the grain boundaries are diffused into adjacent grains and are in a sawtooth shape, so that the alloy needs to consume more energy when being fractured, and the fracture toughness of the alloy is improved. Mechanical property tests show that the tensile strength, the yield strength, the elongation and the fracture toughness of the alloy are 786MPa, 717MPa, 9 percent and 36 MPa.m1/2. Therefore, the plasticity and the toughness of the prepared aluminum alloy are greatly improved.
Example 3 (addition of 18% low alloyed aluminium alloy powder)
The difference from example 1 is that: the addition of the low-alloying aluminum alloy powder is 18 percent, and the spray deposition billet is subjected to densification extrusion and peak aging treatment.
After 18% low-alloying aluminum alloy powder is added into the billet, the grain boundary is similar to the strength 1 and 2 on the whole and takes a sawtooth shape, so that the alloy needs to consume more energy when being fractured, thereby improving the fracture toughness of the alloy. Mechanical property tests show that the tensile strength, the yield strength, the elongation and the fracture toughness of the alloy are 780MPa, 707MPa, 8 percent and 33 MPa.m1/2. Therefore, the plasticity and the toughness of the prepared aluminum alloy are greatly improved.
The foregoing is only a preferred embodiment of the present invention, and it should be noted that, for those skilled in the art, various modifications and decorations can be made without departing from the technical principle of the present invention, and these modifications and decorations should also be regarded as the protection scope of the present invention.

Claims (5)

1. The preparation method of the ultrahigh-strength high-toughness aluminum alloy is characterized by comprising the following steps of:
1) weighing the raw materials according to the chemical components Al- (10-14) Zn- (1.8-3.2) Mg- (0.8-2.0) Cu- (0.15-0.4) Zr- (0.05-0.3) Mn- (0.05-0.3) Ni of the designed ultrahigh-strength and high-toughness aluminum alloy: zn; mg; cu; zr; mn; ni; al; wherein, Cu adopts Al-50Cu intermediate alloy, Ni adopts Al-20Ni intermediate alloy, and the rest is pure metal;
2) putting the weighed pure Al, Al-50Cu intermediate alloy and Al-Ni intermediate alloy into a medium-frequency induction furnace, electrifying and heating until metal in a crucible is melted, heating the melt to 720-740 ℃, adding Zr particles and pure Mn sheets, fully stirring, heating the melt to 800-820 ℃, pressing pure Zn and pure Mg by a graphite pressure spoon after power failure, fully stirring, and heating the melt to 720-750 ℃;
3) adopting proper amount of refining agent and alterant and C2Cl6The degassing agent is used for modifying and refining the melt; after treatment, slagging off the melt, then standing the melt for 10-15 min, and raising the temperature of the melt to 810-850 ℃;
4) pouring the melt into a spray deposition device, simultaneously opening a powder feeding device, feeding low-alloy aluminum alloy powder with the content of 5-30% into a spray deposition atomizing cone, and performing spray deposition to form a billet;
the low-alloying aluminum alloy powder in the step 4) adopts one or more of 7075 aluminum alloy powder, 7055 aluminum alloy powder or pure Al powder;
5) carrying out extrusion densification treatment on the spray deposition billet, wherein the extrusion ratio is 8-10: 1, the extrusion temperature is 420-450 ℃;
6) carrying out peak aging heat treatment on the bar stock, wherein the heat treatment process is solid solution treatment: keeping the temperature of 445-455 ℃ for 0.5-1.5 h and keeping the temperature of 470-480 ℃ for 1-3 h, and then performing water quenching at room temperature; aging treatment: keeping the temperature at 110-130 ℃ for 23-25 hours.
2. The method of claim 1, wherein: the refining agent in the step 3) is HGJ-1, the modifier is HGPB-1, and the weight percentage of the refining agent and the modifier is 0.4-0.6%.
3. The method of claim 1, wherein: the low-alloying aluminum alloy powder in the step 4) needs to be pretreated before being added so as to remove water and gas attached to the powder.
4. The method of claim 1, wherein: the extrusion ratio of the step 5) is 9: 1.
5. the method of claim 1, wherein: solution treatment in the step 6): preserving heat at 450 ℃ for 1h +475 ℃ for 2h, and carrying out aging treatment: the temperature is kept at 120 ℃ for 24 hours.
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